TW200911847A - Polyolefin compositions and articles prepared therefrom, and methods for making the same - Google Patents

Abstract

The invention provides a composition comprising at least the following: an olefin multi-block interpolymer, a functionalized olefin-based polymer, and a thermoplastic polyurethane. The invention also provides for articles prepared from the inventive compositions and for methods for making the same.

Description

200911847 Nine, invention description: L invention shoulder technology field:! CROSS REFERENCE TO RELATED APPLICATIONS This application claims the benefit of U.S. Patent Application Serial No. 60/952,425, filed on Jul. 27, 2007, and U.S. Patent Provision No. 60/952,272, filed on July 27, 2007. Priority is hereby incorporated by reference in its entirety. FIELD OF THE INVENTION The present invention provides a composition comprising: (a) at least one olefin multi-block 10 heteropolymer; (b) at least one functionalized olefin-based polymer; and at least one thermoplastic polyurethane. BACKGROUND OF THE INVENTION Polyolefins, a class of materials, have a relatively poor adhesion and compatibility with relatively polar polymeric materials. In most instances, a separate binder is required to bond the polyolefin to polar substrates such as polyesters, polyamines, polyurethanes, and the like. Similarly, it is essentially necessary to use a third component compatibilizer to prepare a satisfactory melt blend of the polyolefin with other other polar thermoplastic materials. However, a significant amount of compatibilizer 20 is typically required to maintain intimate blending of the polyolefin and the polyurethane. In North America, approximately 25 million pounds of flexible polyvinyl chloride (f_pvc) is used to form sheets for use in the automotive industry, such as equipment and door panels. This sheet can be painted in a striate shape and mated with other inner lining components. Automotive application sheets must meet a number of applications. The main end-use requirements include _low gloss value, high 200911847 surface scratch/trace resistance, high heat resistance and good low temperature impact. In addition, the sheet must have good adhesion to the polyurethane layer of any of the intermediates, e.g., a foam layer for automotive sheeting to provide a softening or cushioning effect. 5 International Patent WO 00/63293 discloses a thermoplastic polyurethane/smoke-graft polymer blend with an optional compatible polymer. The compatible polymer is a modified polyolefin selected from the group consisting of ionomers having an unsaturated organic compound in the main chain or side chain, or block and graft olefin polymers. European Patent Application No. 0437794 A1 discloses a thermoplastic compatible blending composition comprising: (A) 15 to 60 weight percent polyolefin, (b) 30 to 70 weight percent thermoplastic polyamine phthalate, And (C) from 1 to 35 weight percent of at least one modified polyolefin, defined as having one selected from the group consisting of a carboxylic acid, a carboxylic acid ester, a carboxylic acid anhydride, a carboxylate, a decylamine, and a ring in the main chain or side chain. A random, block or graft olefin copolymer of a functional group of an oxy group, a hydroxyl group, or a decyloxy group. U.S. Patent No. 6,251,982 discloses a compounded rubber composition comprising: (a) a hydrogenated, polydiene diol-based polyamino phthalate having a hard bond content of 10% or more. (b) - a non-polar extender oil in an amount of from 10 to 400 phr; and/or (C) at least one thermoplastic resin in an amount of from 5 to 100 phr. U.S. Patent No. 5,578,680 discloses a vibration absorbing elastomer composite 20 comprising: (A) 10 to 60% by weight of at least one thermoplastic resin selected from the group consisting of a dilute hydrocarbon polymer, an ethylene-unsaturated ester copolymer, and a group of natural rubber components, and (B) a 9 〇 4 % by weight of a polyurethane resin in the in-situ molten thermoplastic resin (A) by reacting a polyisocyanate with a polyol And made. The polyurethane (B) has a nitrogen atom content of 3 wt% and has a dissolution parameter of at least 2.5 higher than that of the thermoplastic resin in 200911847, and wherein the composite has a Ταηδ of at least 1.0 at 20 °C. U.S. Patent No. 4,883,837 discloses a thermoplastic compatible blend composition comprising from about 15 to about 60 weight percent of a polyolefin, from about 30 to about 570 weight percent of a thermoplastic polyurethane, and from about 10 Up to about 35 weight percent of at least one modified polyolefin, defined as having one selected from the group consisting of a carboxylic acid, a carboxylic acid ester, a carboxylic acid anhydride, a carboxylate, a decylamine, an epoxy group, a hydroxyl group, in the main chain or side chain, Or a random, block or grafted olefin copolymer of a functional group of a decyloxy group. U.S. Patent No. 4,198,327 discloses a composition for bonding a polar material to the following: (a) from 99 to 70 parts by weight of a modified crystalline polyolefin having an carboxylic acid selected from the group consisting of unsaturated carboxylic acids The monomer of the acid and its anhydride, ester, amidamine and metal salt is grafted, and the crystallized polyolefin has a crystallinity of at least 25% as measured by X-ray analysis, and contains the crystalline polyolefin and the From 0.0001 to 3% by weight of the graft monomer of the total amount of 15 monomers; and (b) from 1 to 30 parts by weight of the hydrocarbon elastomer. U.S. Patent No. 5,705,565 discloses a thermoplastic polymer blend comprising at least one thermoplastic polymer and a substantially linear ethylene polymer having at least about 0.01 weight percent olefination unsaturation to less than 20 The unsaturated organic compound at the position of the carbonyl group is grafted. The thermoplastic polymer may be selected from the group consisting of polyurethanes, polycarbonates, polystyrenes, polyesters, epoxies, polyamines, polar-containing polyolefins, acrylonitrile-butadiene-styrene. a mixture of copolymers and the like. European Patent Application No. 0 657 502 A1 discloses a thermoplastic composition 7 200911847 which contains a mixture of the following components: (a) - block copolymerized oxime ester, monoblock copolyether guanamine and/or polyamine decanoic acid Ester, (b) - a thermoplastic incompatible with (a) - co- or tri-polymer, and (c) a compatibilizer. The compatibilizer is selected according to the nature of component (b). It has a chain link 5 which is compatible with component (b) and preferably identical and a reactive group which is compatible or interactive with component (a). The reactive group can be grafted to the chain using a grafting monomer having at least one α- or/5-alkylated unsaturated carboxylic acid and anhydride, and the like. U.S. Patent No. 6,414,081 discloses a compatible blend comprising: (a) a non-polar thermoplastic elastomer comprising a thermoplastic polyolefin homopolymer or copolymer and a fully crosslinked or partially crosslinked And olefinic rubber, and (b) a polar thermoplastic polymer selected from the group consisting of thermoplastic polyurethane (TPU), gas-containing polymer, fluoropolymer, polyester, acrylonitrile-butadiene- a styrene copolymer 'styrene-acrylonitrile copolymer, styrene·maleic anhydride copolymer, polyacetal, polycarbonate, or polycyclobenzene; and (c) a compatible 15 agent, a condensation copolymer formed from (1) 10 to 90 weight percent of a functionalized olefin polymer and 90 to 10 weight percent of polyamine, based on the total weight of the functionalized polymer and polyamine, or (ϋ) a blend of a functionalized olefin polymer and a polyamine, or a mixture of (iii) (i) and (ii). U.S. Patent No. 6,469,099 discloses a blend of a fluorinated polymeric hydrocarbon and a thermoplastic polyamino 20 carboxylic acid ester which is compatible with an isocyanate reactive group containing a low concentration of polymeric hydrocarbon. This compatibilizer can be prepared by reacting a modified polymer having a pendant group or an amine-reactive group with a hydroxylamine, a diamine, or a polyether monoamine. The compatible blend may further comprise a non-τρϋ processed thermoplastic to form a thermoplastic blend compatible with the polymerized hydrocarbon and non-TPU. 2009-11847 International Publication No. WO 00/63293 discloses a polymer composition comprising a thermoplastic polyurethane, and a first olefin graft polymer, the graft polymer comprising at least a first graft base And at least a second grafting group, the first grafting group is a monoalkyl group, which promotes cross-linking of the grafted elastomer in the presence of moisture, and the second grafting group is a An unsaturated organic compound which, prior to grafting, contains at least one thinning unsaturation and a polar functionality to promote the compatibility of the olefin with the thermoplastic urethane. U.S. Patent No. 5,902,854 discloses the composition comprising an ethylene heterogeneous copolymer such as a linear or substantially linear ethylene heteropolymer and polydidecyloxyxanane. The composition may further comprise an ethylene homopolymer or a heteropolymer grafted with a maleic anhydride or a cis succinic anhydride group. This composition has good anti-wear properties without sacrificing the friction coefficient. U.S. Patent No. 4,397,916 discloses a laminated multilayer structure which is a combination of (A)-layer graft-modified vinyl resin grafted with an unsaturated carboxylic acid or a functional derivative thereof, and a layer (A) contacting (B) an oxygen- or nitrogen-polar resin layer or a metal layer. Part of this layer (A) is characterized by the graft-modified vinyl resin having a composition of (i) 1 to 100 wt%, which is at least one having from 3 to 30 carbon atoms containing from 〇 to 15 mol% The α-olefin is an ethylene polymer derived from a comonomer and (ii) 99 to 〇wt% of an unmodified ethylene polymer, and 2% of which contains 0 to 50 mol% of at least one having 3 to 3 〇 carbon The atomic heart olefin is a comonomer. International Publication No. WO 96/27622 discloses a process for the manufacture of a nucleophilic amine functionalized polyolefin by reacting a polymer having an electrophilic functional group with a diamine having an amine end group, which has a different Reactivity. 200911847 The nucleophilic amine functionalized polyolefin has the composition: polyolefin-X-R1-NHR2, wherein X is selected from the group consisting of imine, decylamine, scutellin or amine, and R1 is a divalent organic group 'R2 Η or monoalkyl. The nucleophilic amine functionalized polyolefin can be used as a compatibilizer, binder, a dyeable material, and a dyeing improver. International Publication No. WO 93/02113 discloses a graft polymer comprising reactive amine functionality and which is prepared by: (a) providing a thermoplastic polymer which contains at least one sufficient to react with a primary amine group An electrophilic functional group; and (b) is fused to a compound containing a -first amine and a primary amine having a reactivity substantially equal to or less than that of the primary amine. Crosslinking can be substantially avoided by utilizing a diamine containing a chemical compound. Modifiers and compatibilizers using a graft polymer as a polymer composition are disclosed. International Publication No. WO 03/008681 discloses a fiber having improved moisture resistance at elevated temperature, comprising at least two elastic polymers, one polymer being heat-curable and the other being heat-resistant polymer. The thermal polymer comprises at least a portion of the outer surface of the fiber. The fiber essentially has a dual component and/or a pair of core/sheath types. Basically, the core comprises an elastomeric thermoplastic urethane, and the sheath comprises a homogeneous branched polyolefin, preferably a homogeneous branched substantially linear ethylene polymer. A fiber component can contain a monofunctional polyethylene. (See also WO 03/008680). Examples of other compositions having a functional component are disclosed in U.S. Patent No. 5,623,019; U.S. Patent No. 6,054,533; U.S. Patent No. 5,578,680; EP 1672046; EP 0734419B1; EP 0657502A1. Other functionalized polymers and/or compositions are disclosed in International Publication No. 10 200911847 WO 99/02603 and U.S. Patent Publication No. 2/4/6744. There is still a need for low cost polyolefin compositions which can be used as good binders for polar substrates such as substrates from polyurethanes, polycarbonates and polyamines. It is further desirable that the composition be used in an overmolding mold and that provides adhesion to a polar substrate. These needs or portions of others have been met by the following invention. The need for a low cost polyolefin is also retained to further comprise a polyamine phthalate and/or a low amount of compatibilizer polyolefin composition, preferably less than 1 weight percent. If the composition can be used as a good adhesion agent for a polar substrate, such as a substrate formed of a polyurethane carbamide, a polycarbonate, and a polyamide substrate, it is more advantageous. If it can be made with high surface energy and good adhesion (•Responsible items such as y materials and membranes are more favorable. There is a further step-by-step requirement for low-cost compatible exchanges with improved heat Aging performance, and is particularly suitable for automotive interior applications that experience high temperatures (eg, up to 12 〇. 其. The advantage of further -15 steps is that this composition can be used as a good binder for polar substrates. Other potential Applications include automotive interior applications (thermoformed outer layers), which provide at least J's luxurious texture, low gloss, and improved trace reproducibility required for heat forming processes under negative pressure. Or a part of the other is satisfied by the following invention. 2. It is also necessary to develop a polyolefin composition containing a polyurethane component and to have the most J amount of compatibilizer or other form of stability to maintain the composition. The stability of the polymer phase, and its high surface energy and good adhesion. These needs or other parts have been satisfied by the following invention. There is a low compatibility with improved, low cost. Agent polyolefin/polyamine 200911847 carboxylic acid The composition is preferably less than 1% by weight based on the total weight of the composition, and is useful for articles having high surface energy and good adhesion properties, such as sheets and films, and preferably greater than 30dyne/cm. A further step in the need for a low cost compatible composition is an improved thermal aging of 5 旎 and is particularly suitable for use in automotive interiors that experience enthalpy (eg, up to 12 〇. Application. A further step-by-step requirement for this composition is that it can be used in automotive interior applications (thermoformed outer layer) and it provides at least the following properties: a luxurious texture, lower gloss and % heat under negative pressure Improved trace reproducibility required to form the process. Additional need for a suitable thermoplastic polyolefin composition that can be used to form sheets that do not require topcoating of the polyurethane to control gloss or scratches And it has good adhesion to polyamino phthalate foam. It is also necessary to develop a weather-resistant, low-gloss and/or good scratch-resistant sheet which has good properties for PUS foam, PU adhesive and coating. Adhesiveness. More suitable for thermoplastics A polyolefin composition which can be used to form a film and injection molding articles. Such requirements and other 15 persons by the following part of the present invention is satisfied.

SUMMARY OF THE INVENTION: SUMMARY OF THE INVENTION The present invention provides a composition comprising at least the following: A) an olefin multi-block heteropolymer; 20 B) a monofunctional olefin polymer; and C) a thermoplastic polyamine Acid ester. BRIEF DESCRIPTION OF THE DRAWINGS Figure 1 illustrates the melting point of several ethylene/α-olefin multi-block heteropolymers (polymers of the invention) and comparative polymers (traditional random and Ziegler_Natta) 12 200911847 as a function of density. Figure 2 does not illustrate the function of the thermal refining "DSC Tm _ CrystafTc" for several polymers. Figure 3 illustrates the effect of the unoriented film made from a specific olefinic multi-segment heteropolymer and a plurality of random copolymers on the recovery density. Figure 4 graphically illustrates the comonomer content of several random ethylene/1-octene copolymers and multi-block ethylene/1 octane copolymer versus TREF elution temperature. Figure 5 is a graph showing the TREF grade and comonomer content of the multi-coupling copolymer (Example 5) and the comparative copolymer (Example F*). The Fig. 6 diagram does not illustrate the storage modulus and temperature of a plurality of multi-block copolymers (polymers of the invention) and comparative random copolymers. Figure 7 does not illustrate TMA (thermomechanical analysis) data and flexible modes of multi-block copolymers (polymers of the invention) and certain comparative examples (VersifyTM, ethylene/styrene, η#ΤΜ) Number data. [Embodiment] DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS As discussed, the present invention provides a composition comprising the following: A) an olefin multi-block heteropolymer; B) a functionalized olefin-based polymer; And optionally 20 C) a thermoplastic polyamino phthalate. In another embodiment, the olefin multi-block heteropolymer is an ethylene/α-olefin multi-block heteropolymer having at least one of the following characteristics: (1) an average block index greater than 0 and up to about 丨〇 and a molecular weight distribution Mw / Mn is greater than about [3; or 13 200911847 (2) at least one molecular component, when eluted between 40 ° C and 130 ° C when using trEF component, Characterizing that the component has a block index of at least 〇5 and up to about 1; or (3) having a Mw/Mn of from about 1.7 to about 3.5, at least one of the five melting points Tm in degrees Celsius, and a density of g/cm3 d, where the values of Tm and d correspond to the following relationships:

Tm > -2002.9 + 4538.5(d) - 2422.2(d)2; or (4) a Mw/Mn' of about 1.7 to about 3.5 and characterized by a heat of fusion of J/g ΔΗ, and a degree of Celsius Δτ, which is defined as the temperature difference between the highest Dsc peak and the highest 10 CRYSTAF peak, where δτ has the following relationship with the value of ΔΗ. For ΔΗ greater than 0 and as high as 130 J/g, ΑΤ>-0.1299(ΔΗ)+ 62.8 for ΔΗ greater than 130 J/g, AT 248 ° C, where the CRYSTAF peak is determined using at least 5 percent polymer accumulation, 15 and if less than 5 percent of the polymer has an identifiable CRYSTAF peak, the CRYSTAF temperature is 30 °C; or (5) - elastic recovery Re' as a percentage of the compression molded film of the ethylene/α-olefin heteropolymer at 300% strain and 1 cycle, and a density d of g/cm3, wherein When the ethylene/α-olefin heteropolymer is substantially uncrossed, the values of 'Re and d satisfy the following relationship: Re >i481-1629(d); or (6) - molecular component 'when using TREF When fractionated, when eluted between 40 C and 130 C, the characteristic is that the component has a comparable random B-sparse than the elution at the same temperature. The copolymer component is at least 5 percent higher than the 200911847 mole comonomer content, wherein the comparable random ethylene heteropolymer has the same comonomer and has a melt index, density, and molar comonomer content ( Based on the total polymer) is within 10% of the ethylene/(X-olefin heteropolymer; or, 5 (7) is stored at 25 ° C, G' (25 ° c), and at 100 ° c Storage modulus, G' (100 ° C), where G' (25 ° C) versus G' (100 ° C) ratio is between about 1:1 to about 9: 1. This olefin multi-block heterogeneous The copolymer may have at least two of the combinations described herein. In one embodiment, the functionalized olefinic polymer, also referred to as a polyolefin, is comprised of an olefinic polymer and at least An organic compound selected from the group consisting of an "amine-containing compound", a "hydroxyl-containing compound", an "imine-containing compound", an "anhydride-containing compound", or a "carboxylic acid-containing" compound. In another embodiment, The anhydride compound is maleic anhydride. 15 In another embodiment, the functionalized olefin polymer In an amount of less than or equal to 20 weight percent of the total weight of the composition. In another embodiment, the functionalized olefinic polymer is present in an amount less than or equal to 10 weight percent of the total weight of the composition. In another embodiment, the functionalized olefin-based polymer is present in an amount less than or equal to 5 weight percent to 20 parts by weight based on the total weight of the composition. In another embodiment, the functionalized dilute hydrocarbon polymer is present in an amount greater than or equal to 20 weight percent based on the total weight of the composition. In another embodiment, the functionalized dilute hydrocarbon polymer is present in an amount greater than or equal to 30 weight percent based on the total weight of the composition. In another embodiment, the functionalized alkene 15 200911847 hydrocarbon polymer is present in an amount greater than or equal to 40 weight percent of the total weight of the composition. In another embodiment, the functionalized olefin-based polymer has a density of from about 0.85 g/cc to about 0.91 g/cc. In another embodiment, the at least one 5 functionalized olefin-based polymer has a density of from about 0.84 g/cc to about 0.93 g/cc. In another embodiment, the at least one functionalized olefin-based polymer has a density of from about 0.85 g/cc to about 0.93 g/cc. In another embodiment, the at least one functionalized olefin-based polymer has a density of from about (λ 8 4 g / cc to about 0. 90 g/cc. 10 In another embodiment, the functionalized The olefin-based polymer has a melt index (12) of from 0.1 g/ΙΟ min to 100 g/ΙΟ min, preferably from 0.2 to 100 g/ΙΟ min. In another embodiment, the functionalized olefin system The polymer has a melt index (ι2) of from 1 g/ιο分钟 to 5 〇 gno. In another embodiment, the at least one functionalized olefin-based polymer has a melting 15 index (12) of 1 g/ΙΟ min to 10 g/ΙΟ min. In another embodiment, the at least one functionalized olefin-based polymer has a melt index (12) of from 1 g/10 min to 20 g/min. In another embodiment, the functionalized olefin polymer is formed from a vinyl polymer. In yet another embodiment, the vinyl polymer is a methene/(X-olefin heteropolymer). In one embodiment, the (X-olefin is a C3-C20 alpha-olefin, and preferably a C3-C10 a-olefin. In yet another embodiment, the alpha-lean hydrocarbon is Free in the group consisting of 1-propene, 1-butene, 1-hexene and 1-octene, and preferably 1-butene and 1-octene. In another embodiment, for forming functional groups The ethylene/α-olefin heteropolymer of the olefin-based polymer 16 200911847 further comprises a diene. In another embodiment, the ethylene/α-olefin heteropolymer has a ratio of from 0.85 g/cc to 0.93 g/cc. In another embodiment, the ethylene/α-olefin heteropolymer has a melt index (12) of from 0.01 g/10 min to 1500 g/10 min. 5 In another embodiment, The ethylene/α-olefin heteropolymer forming the functionalized olefin-based polymer is a homogeneous branched linear heterogeneous copolymer or a homogeneous branched substantially linear heterogeneous copolymer. In another embodiment, the functionalized olefinic system is formed. The ethylene/α-olefin heteropolymer of the polymer homogenizes the branched substantially linear heterogeneous copolymer. 10 In another embodiment, the functionalized olefin-based polymer is formed from a propylene-based polymer. In another embodiment, The propylene polymer is a propylene/ethylene heteropolymer or a propylene/(X-olefin) In another embodiment, the propylene-based polymer is a propylene/α-dilute hydrocarbon heteropolymer, wherein the α-dilute hydrocarbon is a C4-C20 α-indole hydrocarbon, and preferably a C4 -C10 alpha-ene 15 hydrocarbon. In another embodiment, the alpha olefin is selected from the group consisting of 1-butene, 1-hexene, and 1-octene. In another embodiment, The propylene rhodium-olefin heteropolymer has a density of from 0.85 g/cc to 0.93 g/cc. In another embodiment, the propylene/α-olefin heteropolymer has a melt index (12) of from 0.01 g/10 minutes to 1500 g/10 minutes. In another embodiment, the propylene 20 polymer is a propylene/ethylene heteropolymer. In still another embodiment, the propylene/ethylene heteropolymer has a density of from 0.85 g/cc to 0.93 g/cc. In another embodiment, the propylene/ethylene heteropolymer has a melt index (12) from 0.01 g/10 minutes to 1500 g/10 minutes. In another embodiment, the functionalized olefin-based polymer is formed from a monoene 17 200911847 hydrocarbon multi-block heteropolymer. In another embodiment, the functionalized olefin-based polymer is formed by a process comprising the steps of: (1) grafting at least one of the olefin-based polymer chains comprising at least one "amine-reactive" group a compound to form a grafted olefin-based polymer; (2) reacting a grade-secondary diamine with the grafted olefin-based polymer; and wherein the step (2) is carried out without grafting the grafted olefin-based polymer Subsequent to the step (1), and two of the steps should be carried out in a melt reaction. In still another embodiment, the primary-secondary diamine is N-ethylethylenediamine, N-phenylethylenediamine, N-phenyl-1,2-phenylene-diamine, N Selected from the group consisting of phenyl-1,4-phenylenediamine and N-(2-hydroxyethyl)-ethylenediamine. In another embodiment, the functionalized olefin-based polymer comprises the following functional groups covalently bonded to the olefin-based polymer chain:

N-RrNHR2 Λ > 15 wherein "NKNHR," may be derived from a primary-secondary diamine selected from the group of compounds having the following structure (I): H2N-Ri-NH-R2 (7) wherein R! a divalent hydrocarbon group, preferably selected from the group consisting of alkenyl groups and phenylene groups, and preferably -CH2CH2-, -p-phenylene-, -o-phenylene-, and 20 R2 are contained A monovalent hydrocarbon group of at least 2 carbon atoms, and optionally substituted with a group having 18 200911847 having a hetero atom, which is preferably a monoalkyl or aryl group and more preferably an ethyl or a phenyl group. In one embodiment, the primary-secondary diamine is derived from N-ethylethylenediamine, N-phenylethylenediamine, N-phenyl-1,2-phenylenediamine, N-phenyl- Selected from the group consisting of 1,4-, 5-phenylenediamine and N-(2-hydroxyethyl)-ethylenediamine. In another embodiment, the functionalized olefin-based polymer comprises the following The method of the steps is: 1) functionalizing at least one compound comprising at least [an "amine-reactive" group on the chain of the olefin polymer to form a graft olefin polymer; 10 2) in a solid state, Blending the graftedene in molten form a hydrocarbon-based polymer with at least one primary-secondary diamine; 3) absorbing the primary-secondary diamine onto the grafted olefin-based polymer; 4) reacting the primary-secondary diamine with the grafted olefin The polymer is reacted to form an imine functionalized olefin polymer. 15 In one embodiment, the absorption step is carried out at room temperature. In another embodiment, the blending step is carried out at room temperature. In one embodiment, the at least one functionalized olefin-based polymer is formed by a process comprising the steps of: 1) grafting at least one of at least one 20 "amine-reactive" group on a chain of a dilute hydrocarbon polymer. a compound to form a grafted dilute hydrocarbon polymer; 2) reacting a monoalkanolamine with the grafted olefin polymer; and wherein the step (2) is carried out in the subsequent step without separately grafting the grafted olefin polymer (1) is carried out, and wherein the two steps (1) and (2) are carried out in a melt reaction. In still another embodiment, the alkanolamine is selected from the group consisting of 2-aminoethanol, 2- 19 200911847 amine group 1-propanol, 3-amino-1-propanol, 2-amino-1-butanol, 2-(2-aminoethoxy)-ethanol and 2-aminobenzylmethyl . The group consisting of In another embodiment, the at least one functionalized olefin-based polymer comprises the following covalently bonded to the functional group of the olefinic polymer chain carrier:

N-RrOH Η 5 , wherein "ΝΚΟΗ" may be derived from an alkanolamine selected from the group of compounds having the following structure (II): Η2Ν-R, -OH (π), the center of which is one or two a hydrocarbon group, R, preferably a substituted or unsubstituted alkene 10 group, more preferably a core selected from the group consisting of ethylene, propylene, butylene, and a group consisting of an alkoxy group and a phenyl group. The at least one selected alkenyl group is selected, and more preferably R^-CH(OCH2CH2Me)CH2- or -o-phenylene-CH2-. In still another embodiment, the alkanolamine is selected from the group consisting of 2-aminoethanol, 2-15 amino-1-propanol, 3-amino-1-propanol, 2-amino-1-butanol , a group consisting of 2-(2-aminoethoxy)-ethanol and 2-aminobenzyl alcohol. In another embodiment, the at least one functionalized olefin-based polymer is formed by a process comprising the steps of: 1) grafting at least 20 of the following formulas on a chain of olefin-based polymers in a melt reaction ( Compound of IV) to form a grafted olefin polymer: 20 200911847

2) and heat-treating the grafted olefin-based polymer to form an imine-functionalized olefin-based polymer, and wherein R1 and R2 are each independently hydrogen or a C1-C20 hydrocarbon group, which is linear or branched; R3 is hydrogen or a a C1-C20 hydrocarbyl group which is linear 5 or branched; R4 is a divalent hydrocarbon group which is linear or branched; X is OH or NHR5, wherein R5 is a hydrocarbyl group which is linear or branched, or monohydroxyethyl. In still another embodiment, R1 and R2 are each independently hydrogen or a C1-C10 hydrocarbon group. In another embodiment, R3 is hydrogen or a C1-C10 hydrocarbyl group, and wherein R4 is a divalent hydrocarbyl C1-C20 hydrocarbyl group. In another embodiment, the functionalized olefin-based polymer comprises the following functional groups covalently bonded to the olefin-based polymer chain:

Wherein R1 and R2 are each independently hydrogen or a C1-C20 hydrocarbyl group which is linear or branched; R4 is a divalent hydrocarbon group which is linear or branched; X is OH or 15 NHR5, wherein R5 is a hydrocarbyl group which is linear Or branch, or monohydroxyethyl. In still another embodiment, R1 and R2 are each independently hydrogen or a C1-C10 hydrocarbon group. In another embodiment, R4 is a divalent hydrocarbyl C1-C20 hydrocarbyl group. The functionalized olefin-based polymer can have a combination of at least two embodiments of the invention described herein. In another embodiment, the thermoplastic polyaminophthalate comprises a chemical unit derived from (1) a polyester and (2) an aromatic diisocyanate or an aliphatic diisocyanate. In another embodiment, the thermoplastic polyaminophthalate 5 comprises a chemical unit derived from a polyester and at least one aromatic diisocyanate. In another embodiment, the thermoplastic polyurethane comprises a chemical unit derived from a polyester and at least one aliphatic diisocyanate. In another embodiment, the thermoplastic polyamino phthalate comprises from a polyester and 1,3-bis(isocyanatomethyl)-cyclohexane and 1,4-bis(isocyanatomethyl) ) - 10 chemical units derived from a cyclohexane mixture. In still another embodiment, the weight ratio of 1,3-bis(isocyanatoindenyl)-cyclohexane to 1,4-bis(isocyanatomethyl)cyclohexane is about 1 to 1. . In another embodiment, the polyurethane is formed from a polyester comprising monomer units derived from a diol derivative derived from N-octylpyrrolidone. In another embodiment, the polyurethane is formed from a package of polyester comprising monomer units derived from polytetramethylene ether glycol. In another embodiment, the polyurethane is formed from a polyester comprising monomer units derived from a polyether. In another embodiment, the thermoplastic polyurethane is PELLETHANETM polyurethane. In yet another embodiment, the poly S is formed from polycaprolactone. In another embodiment, the thermoplastic polyurethane has a density of from 0.90 g/cc to 1.3 g/cc. In another embodiment, the thermoplastic polyphthalic acid decanoate has a melting index (12) from 0.2 g/Torr to 100 g/min. In another embodiment, the thermoplastic polyurethane has a melt index (12) from 1 g/ΙΟ minute to 100 g/ΙΟ minute. In another embodiment 22 200911847, at least one thermoplastic polyurethane has a melt index (I2) from 0.2 g/10 minutes to 1 〇 g/10 minutes. In another embodiment, the at least one thermoplastic polyurethane has a melt index of from n g / 1 〇 min to 1 〇 g / 1 〇 min. In another example, the thermoplastic polyurethane is formed from a monomer unit comprising an alcohol-derived organism derived from N-octylpyrrolidone. In another embodiment, the thermoplastic polyaminophthalate comprises - comprising monomer units derived from polytetradecylene ether glycol. In still other embodiments, the thermoplastic polyurethane comprises a monomer unit comprising a polyether. The thermoplastic 1 amino carboxylic acid vinegar can have a combination of at least two embodiments as described herein. One of the compositions of the present invention may further comprise at least one additive. For example, a composition of the invention may further comprise at least one filler. In another embodiment, 15 the filler is -talc or - talc modified with at least one amine stone surface. In another embodiment, a composition of the present invention may comprise a polar polymer selected from the group consisting of: polyester, polyamine, poly bond, poly-imine, polyvinyl alcohol, polycarbonate S, a combination of polyamine phthalic acid vinegar, polylactic acid, polyamine amide, and the like. 2 〇 In one embodiment, the composition may further comprise a low density polyethylene

(LDPE). In still another embodiment, the LDPE has a swell index from -2 to (10) _ minutes (i9 (rC/2.16 kg). In yet another embodiment, the LDpE has a 〇·5 to 50 g/ 10 minutes (10) port 2 16 炼 smelting index. In yet another embodiment, this L cleave has a melt index from - to 25 coffee minutes (i9 〇 t 23 200911847 / 2.16 kg). In another embodiment The composition has a surface energy greater than or equal to 35 dynes/cm °. One of the compositions of the present invention may comprise a combination of at least two embodiments described herein. The invention also provides an article comprising at least one set of parts Formed by the composition of the present invention. In yet another embodiment, the article is a sheet, carpet, adhesive, wire sheath, cable, protective clothing, automotive parts, shoe assembly, coating or foam laminate, Overpressure molded parts, automotive exterior, cover 10, waterproof clothing, leather objects, roof structure, steering wheel parts, powder coating, powder molding, consumer durables, grips, handles, computers (4), belts, decals , shoe assembly, transfer or timing belt, or fabric. In another embodiment The article is a bonding layer between the extruded sheets, a bonding layer between the extruded films, a bonding layer between the extruded profiles, and a bonding layer between the laminating materials 15 and the bonding between the laminating films. , in the case of a layer, or a bonding layer between any of the foregoing combinations. The invention also provides a film comprising at least a layer formed from the composition of the invention. In another embodiment, The invention also provides a film comprising at least one layer, and wherein at least one layer is formed from the composition of the invention. In another embodiment, the film of the invention has moisture vapor permeation to g/hr/ft2. Also provided is a extruded sheet formed from a composition of the present invention. In still another embodiment, the sheet has a surface energy greater than or equal to 3 〇dyne/cm, preferably greater than or equal to 33 dyne/cm, more Preferably, it is greater than or equal to 24 200911847 at 35 dyne/cm. In another embodiment, the sheet has a thickness from ι米米耳 to 1000 mils, preferably from 15 mils to 50 mils, and more Preferably, the sheet is from 20 m to 100 m. In another embodiment, the sheet is at 12 〇. (: heat aging 500 After an hour (ASTM D-882-02), it still maintains at least 50 percent of the original 5 extensibility, preferably at least 60 percent. The present invention also provides a coating substrate wherein the substrate is formed from one of the compositions of the present invention. In one embodiment, the coating comprises at least one additive selected from the group consisting of acrylic polymers, alkyds, cellulosic materials, and

A group consisting of a melamine resin, a urethane resin, an amine phthalate resin, a polyester resin, a vinyl acetate resin, an epoxide, a polyhydric alcohol, and/or a monool. In another embodiment, the coating is a water based coating. In another embodiment, the coating is an organic solvent based coating. 15 20 The present invention also provides a dispersion comprising the composition of the present invention. In another embodiment, the dispersion further comprises at least one additive selected from the group consisting of acrylic polymers, alkyd resins, cellulosic materials, trimeric amine resins, amino formic resins, and urethanes. A combination of a resin, a polyester resin, a vinyl acetate resin, an epoxide, a polyol, an alcohol, and the like is in a group. In another embodiment, the dispersion is an aqueous dispersion. In another implementation, the dispersion is an organic solvent (10), a dispersion. -=:! for an injection molded article comprising at least one component formed from the composition of the present invention. It comprises a group of the invention comprising: (a) - comprising a polarity. The invention also provides an RF fusion article, at least a component of the formation. The present invention also provides an overmolded article, 25 200911847, a lung formed by the formation of a poly-substance, and (8) a molded multi-layer formed from the composition of the present invention. In an embodiment, the polar polymer is polycarbonate (p c), ABS, PC/ABS or Resistant. The present invention also provides an overmolded article comprising (4) a substrate formed from the composition of the present invention, and (b) a molded composite layer formed from the present invention. In one embodiment, the article is in the form of a grip, handle or strap. The present invention also provides a laminate structure comprising a first layer and a second layer ' and wherein the first layer is formed from a composition of the invention and wherein the second layer is formed from a composition comprising a polar polymer. In another embodiment, one of the layers is in the form of a foam. In another embodiment, one of the layers is in the form of a fabric. In another embodiment, the laminate structure is in the form of a canopy, a waterproof garment or a car skin or steering wheel. In another embodiment, the second layer is formed from a composition comprising polycarbonate. The present invention also provides a molding 15 piece comprising 'the first component and the second component' and wherein the first component is formed of a composition comprising a polar polymer, and wherein the second component is - The composition of the present invention. In another embodiment, the article is in the form of a car skin layer, a decal, a shoe assembly, a conveyor belt, or a consumer product. The invention also provides a shoe article comprising at least one component formed from a composition of the invention. In still another embodiment, the article is selected from the group consisting of: outsole, midsole, outsole, overmoulded parts, natural leather items, synthetic leather items, uppers, laminates , coated objects, boots, shoes, rubber footwear, plastic shoes and other combinations. The invention also provides a thermoformed sheet comprising at least one layer formed from one of the compositions of the present invention. The invention also provides an automotive component comprising at least one layer formed from a composition of the invention. The present invention also provides automotive components, such as an instrument panel or door panel formed from a composition of the present invention. The invention also provides an artificial leather comprising at least one component formed from one of the compositions of the invention. The present invention also provides an artificial waterproof garment comprising at least one component formed from one of the compositions of the present invention. f The present invention also provides an adhesive comprising at least one component formed from one of the compositions of the present invention. The present invention also provides a coated substrate comprising the adhesive of the present invention and at least one component being formed from Kevlar. The invention also provides an article formed from a composition of the invention, and wherein the article has a surface energy greater than or equal to 35 dynes/cm. The article of the present invention may comprise a group 15 of at least two embodiments described herein. The present invention also provides a blown film comprising at least one layer formed from the 'component' of the present invention. In one embodiment, the blown film is an adhesive film. In one embodiment, the blown film is an assembly of an automotive component. In one embodiment, the blown film is an assembly of shoe elements. In yet another embodiment, the shoe assembly is selected from the group consisting of: an outsole, a midsole, a sole, an overmolded article, a natural leather article, a synthetic leather article, an upper, a laminate A combination of objects, coated objects, boots, slippers, rubber footwear, plastic shoes, and the like. 27 200911847 In one embodiment, the blown film is a barrier film. In yet another embodiment, the barrier film is between a fabric and a polyurethane foam. In one embodiment, the blown film is an assembly of a floor article. The present invention also provides an injection molded article comprising at least one set of 5 parts formed from one of the compositions of the present invention. In one embodiment, the composition is in the form of a "blend in press". In another embodiment, the composition is in the form of a blend. The present invention also provides an overmolded article comprising at least one component formed from the composition of the present invention. In one embodiment, the composition is in the form of a "blend in a 10 press." In another embodiment, the composition is in the form of a compounded blend. The invention also provides a process for making a composition of the invention comprising melt mixing components A, B and optionally C. In one embodiment, the intended components are simultaneously mixed. In another embodiment, this expected component 15 is continuously mixed in any order. In another embodiment, this melt mixing is carried out in an extruder. In another embodiment, this melt mixing is carried out in an "in-line" compounding process. The method of the invention may comprise a combination of at least two embodiments described herein. One of the compositions of the present invention may comprise a combination of at least two of the embodiments described herein. An article of the invention may comprise a combination of at least two embodiments described herein. Functionalized olefin-based polymers 1. Outline functionalized olefin-based polymers include, but are not limited to, carboxylic acids, anhydrides, alcohols, amines, epoxides, hydroxyls, isocyanates, and other groups. A functionalized hydrocarbon-based polymer in combination with it. Functionalization can occur along the thin tobacco polymer backbone, at the chain ends, in a block, and/or as a side chain. In one embodiment, the functionalized olefin-based polymer is a monofunctional -5 vinyl polymer, and is preferably a monofunctional ethylene/α-smoke heteropolymer having greater than or equal to 〇 • a melt index of 5 g/io min (〖2), preferably greater than or equal to 1 g/ΙΟ min, and more preferably greater than or equal to 2 g/1 min, as in ASTM D-1238 (190 ° C) , 2_16 kg load) determination. In another embodiment, the functionalized olefin-based polymer is a monofunctional ethylene 10-based polymer, and is preferably a monofunctional ethylene/α-olefinic heterologous copolymer having less than or A melt index equal to 50 g/10 min (ΙΟ, preferably less than or equal to 20 g/ΙΟ min, and more preferably less than or equal to 1 g/i min, as in ASTM D-1238 (190 ° C, 2.16 kg load). In another embodiment, the functionalized olefin polymer is a monofunctional oxime polymer, and preferably a monofunctional ethylene/α-olefin heteropolymer. It has a melt index I from 0.5 g/ΙΟ min to 50 g/ΙΟ min; (12), preferably from 1 g/ΙΟ min to 20 g/ΙΟ min, and more preferably from 2 g/ΙΟ Minutes to 10 g/ΙΟ minutes, as measured by ASTM D-1238 (19〇t:, 2.16 kg load). All individual values and 20 ranges from 0.5 g/l〇 min to 50 g/10 min include In another embodiment, the functionalized olefin-based polymer is a monofunctional vinyl polymer, and preferably a monofunctional ethylene/α_ A hydrocarbon heterogeneous copolymer having a density greater than or equal to 0.84 g/cc, preferably greater than or equal to 0-85 g/cc' and more preferably greater than 〇86 g/cc. In another embodiment, 29 200911847 The dilute hydrocarbon polymer is a monofunctional ethylene polymer, and is preferably a monofunctional ethylene/α-olefin heteropolymer having a density of less than or equal to 0.91 g/cc, preferably It is less than or equal to 0.90 g/cc, and more preferably less than or equal to 0.89 g/cc. 5 In another embodiment, in another embodiment, the functionalized olefinic polymer is monofunctionalized. An ethylene-based polymer, and preferably a monofunctional ethylene/α-dilute hydrocarbon heteropolymer having a density of from 0.84 g/cc to 0.91 g/cc, preferably from 0.85 g/cc to 0.90. g/cc, and more preferably from 0.86 g/cc to 0.89 g/cc. All individual values and sub-ranges from (λ84 g/cc to 0.91 g/cc include 10 and are disclosed in the present specification. In another embodiment The functionalized olefin-based polymer is an amine-functionalized olefin-based polymer, preferably an amine-functionalized ethylene-based polymer, and more preferably an amine-functionalized polymer. In another embodiment, the α-olefin is a C3-C20 α-olefin, preferably a C3-C10 α-ene 15 hydrocarbon, and more preferably propylene, 1- Butylene, 1-hexene or 1-octene. In another embodiment, the functionalized olefin-based polymer is a monohydroxy-functionalized olefin-based polymer, preferably a hydroxy-functionalized vinyl-based polymer. More preferably, it is a monohydroxy-functionalized ethylene Ax-olefin heteropolymer. In still another embodiment, the α-olefin is a C3-C20 α-olefin, preferably a 20 C3-C10 α-olefin, and more preferably propylene, 1-butene, 1-hexene or 1- Octene. In another embodiment, the functionalized olefin-based polymer is a monohydroxy-functionalized olefin-based polymer, preferably a hydroxy-functionalized vinyl-based polymer, and more preferably a hydroxy-functionalized ethylene/α. - an olefin heteropolymer. In still another embodiment, the α-olefin is a C3-C10 α-olefin, preferably C3-C10 α- 30 200911847, and more preferably propylene, butadiene, dipyridyl or Rare. In one embodiment, the functionalized vinyl polymer is an anhydride-functionalized ethylene-based polymer and is preferably an anhydride-functionalized ethylene/α·smoke heteropolymer having greater than or equal to 〇 The smelting index of 1 g/1 〇 minute (6) is greater than or equal to 〇·5 g/1 〇 min, and more preferably greater than or equal to 】 coffee minutes, such as ASTM D_1238 (19 (rc, 2 16 kg) Load. In another embodiment, the functionalized vinyl polymer is an anhydride-functionalized vinyl polymer, and is preferably an anhydride-functionalized ethylene/α-olefin heteropolymer having less At or equal to 50 g / l 〇 minutes of the melt index mountain), preferably 10 is less than or equal to 20 g / ΙΟ minutes, and more preferably less than or equal to 1 〇 g / 1 〇 minutes, such as eight 8 ^1〇-1238 (190. (:, 2.16 let name load) is measured. In another embodiment, 'this functionalized vinyl polymer is - a functionalized vinyl polymer, and preferably one An anhydride functionalized ethylene/α-olefin heteropolymer having a density greater than or equal to 0.84 g/cc, preferably greater than 15 or equal to 85 g/cc, and Preferably, it is greater than 0 86 g/cc. In another embodiment, the functionalized ethylene polymer is an anhydride-functionalized vinyl polymer, and preferably an anhydride-functionalized ethylene/α-olefin A heterogeneous copolymer having a density of less than or equal to 0-91 g/cc, preferably less than or equal to 〇9〇g/cc, and more preferably less than or equal to 0.89 g/cc. In one embodiment, the functionalized ethylene-based polymer is an anhydride-functionalized vinyl-based polymer, and is preferably an anhydride-functionalized ethylene/α-olefin heteropolymer having 'from 0.84 g/cc to The density of 〇·91 g/cc is preferably from 0.85 g/cc to 0.90 g/cc' and more preferably from 0.86 g/cc to 0.89 g/cc. From 〇.84 g/cc to 0.91 g/cc The individual values and the sub-ranges are included and disclosed in the specification of 31 200911847. 2 · Examples of olefin-based polymer olefin-based polymers used as base polymers for functionalized olefin-based polymers include high-density polyethylene (HDPE) ), low density 5 degree polyethylene (LDPE), linear low density polyethylene (LLDPE), linear ethylene / alpha olefin heteropolymer, substantially linear ethylene / alpha olefin heterogeneous 'Organic multi-block heteropolymers. Suitable base polymers also include polypropylene homopolymers and propylene copolymers' and other olefin-based polymers, such as those formed from at least one C4-C20 alpha-olefin. The olefin-based polymer may optionally comprise a copolymerizable conjugated diene, a non-conjugated diene and/or a vinyl monomer. (1) A vinyl polymer of a functionalized olefin polymer, preferably maleic anhydride The grafted polymer includes the AmplifyTM polymer available from The Dow Chemical Company. 15 His examples include FUSABOND (obtained by DuPont), EXXELOR (obtained by ExxonMobil) and poly BOND (obtained by Chemtura). In one embodiment, the maleic anhydride graft polymer comprises from 3% by weight to 1.5% by weight of the grafted cis-butenedoic anhydride. In still another embodiment, the maleic anhydride graft polymer is a maleic anhydride grafted vinyl polymer. In still another embodiment, the cis-buthanic acid-grafted polymer is a maleic acid-grafted ethylene/(X-olefin heteropolymer). As discussed above, 'suitable vinyl-based polymers include, For example, high density 32 200911847 polyethylene (HDPE), linear low density polyethylene (LLDPE), ultra low density polyethylene (ULDPE), homogeneous branched linear ethylene polymer, homogeneous branched substantially linear ethylene polymer (ie, homogeneous branch long chain Branched ethylene polymer), and ethylene or olefin multi-block heteropolymer. 5 High density polyethylene (HDPE) which can be used as a polyolefin resin has a density substantially from about 0.94 to about 〇_97 g/cc. HDPE Commercial examples have been readily available from the market. Other suitable ethylene polymers include low density polyethylene (LDPE), linear low density polyethylene (LLDPE), and linear non-low density poly(ethylene (VLDPE). Basically This low density polyethylene (LDPE) is made using free radical polymerization conditions under high pressure 10. The low density polyethylene has a density substantially from 0.91 to 0.94 g/cc. Linear low density polyethylene (LLDPE) is the opposite Traditional L DPE, LLDPE is characterized by a small number of long chain branches, if any. The process for producing LLDpE is known in the art and commercially available as a polyolefin grade 15 grease. Typically, LLDPE is in a gas phase fluidized bed reactor. Or liquid phase solution process - reactor production, using Ziegler-Natta catalyst system. \ This linear low density polyethylene (LLDPE), ultra low density polyethylene (ULDPE), homogeneous branched linear ethylene heteropolymer, homogeneous branch substantially linear The acetamrene heteropolymer or the olefin multi-block heteropolymer is substantially 20-incorporated into at least one α-olefin. As used herein, the term "hetero-copolymer" means that the polymer may be a copolymer, - three a polymer or any polymer having at least one polymerized monomer. Monomers usable for copolymerization with ethylene to produce a heteropolymer include C3-C20 alpha-olefins, more preferably C3-C10 ex-olefins, and especially Propylene, 1-butene, 1-pentene, hexene, 4 methyl 丨 戊 pentene, _ 33 200911847 Heptane and 1-octene. Particularly preferred comonomers include propylene, 1-butene, 1-hexene and 1-octene. Overall fit The ethylene polymer has a melt index (12) of less than or equal to 1500 g/10 min, preferably less than or equal to 1000 g/min 5 minutes', more preferably less than or equal to 500 g/min, even more Preferably, it is less than or equal to 100 g/ΙΟ minutes, and most preferably less than or equal to 50 g/10 minutes, which is measured by ASTM 1238 under the condition of 190 ° c / 2.16 kg. Suitable ethylene-based heteropolymer Commercial examples include ENGAGETM, ATTANETM, AFFINITYTM, 10 DOWLEXTM, ELITETM from The Dow Chemical Company; EXCEEDTM and EXACTtm from Exxon Chemic al; and compounds from Mitsui Chemical. The terms "homogeneous" and "homogeneous branch" are used to mean an ethylene/α-olefin heteropolymer, wherein the α-olefin comonomer is randomly distributed in a specific polymer of 15 molecules, and substantially all of the polymer molecules have The same ethylene-on-comonomer ratio. The homogeneous branched ethylene heteropolymers useful in the practice of the invention include linear ethylene heteropolymers and substantially linear ethylene heteropolymers. In the homogeneous branched linear ethylene heteropolymer, an ethylene polymer derived by polymerizing a comonomer into a heterogeneous copolymer, which lacks a long-chain branch but does have a short-chain branch, and which is in the same polymer chain and Different polymer chains are homogeneously distributed. That is, the homogeneous branched linear ethylene heteropolymer lacks long chain branching only when a linear low density polyethylene polymer or a linear high density polyethylene polymer is produced using uniform branch distribution polymerization. A commercial example of a homogeneous branched linear ethylene/α-olefin heteropolymer is included by 34 200911847

TAFMERtm polymer supplied by Mitsui Chemical and EXACTTM polymer supplied by ExxonMobil Chemical. The substantially linear acetylated heteropolymers useful in the present invention are described in U.S. Patent Nos. 5,272,236, 5,278, 272, 6, 054, 544, 6, 335,410, and 5, 723, 810, the disclosures of each of which are incorporated herein by reference. The substantially linear ethylene heterogeneous copolymer is one in which the copolymerized precursor is randomly distributed in a specific polymer molecule and substantially all of the polymer molecules in the heterogeneous copolymer have the same ethylene/comonomer ratio. Further, the substantially linear ethylene heterogeneous copolymer is a homogeneous branched ethylene heteropolymer having long chain branches. The long chain 10 branches have the same comonomer distribution as the polymer chain link and may have the same length as the polymer backbone length. Basically, "substantially linear," refers to an average of 0.01 long chain branches per 1000 carbon to a long chain branched polymer per 1000 carbons. The length of the long chain branches is greater than by incorporating a comonomer into the polymer. The short chain branches formed by the chain frame have a long carbon length. 15 Some polymers may be substituted by 0.01 long chain branches per 1000 carbon to 1 long chain branch per 1000 carbons' or from 0.05 long chain branches per 1000 carbon to 1 inch. Substituted by the long-chain branch of hydrazine carbon, it is substituted with 0.03 long chain branches per 1000 carbon to 1 long chain branch per carbon. Commercial examples of substantially linear polymers include ENGAGETM polymers and AFFINITYTM polymers (all available from Dow) Chemical Company) 20 This substantially linear ethylene heterogeneous copolymer forms a unique class of homogeneous branched ethylene polymers, which are substantially different from the known conventional, homogeneous branched linear acetylated heterocopolymers, such as those described in Elston, USA. U.S. Patent No. 3,645,992, the disclosure of which is incorporated herein by reference in its entirety in its entire entire entire entire entire entire entire entire entire entire entire entire entire entire entire entire- Low density polyethylene (UldPE), linear low density polyethylene (LLDPE) or high density polyethylene (HDPE) are different types; and they are different from high-branched polyethylenes that start with high pressure and free radicals. Low density polyethylene (LDPE), ethylene-acrylic acid (EAA) copolymer and 5 ethylene vinyl acetate (EVA) copolymer. The homogeneous branched, substantially linear ethylene heteropolymer used in the present invention has excellent handleability even It has a relatively narrow molecular weight distribution. Surprisingly, according to ASTM D 1238, the melt flow rate (11()/12) of the substantially linear ethylene heteropolymer can vary widely and is substantially independent of the molecular weight distribution 10 (Mw/Mn). *MWD). This surprising property is completely different from the traditional homogeneous branched linear ethylene heterogeneous copolymer, as described in U.S. Patent No. 3,645,992, and the heterogeneous branch of the traditional 2々161"-like linearization of polymerization. Polyethylene heterogeneous copolymers, as described in U.S. Patent No. 4,076,698 to Anderson et al., which is different from the substantially linear ethylene heteropolymer, a linear ethylene olefin heteropolymer (whether homogeneous or heterogeneous) Rheological properties, such as when the sub-quantity distribution increases, the 11()/12 value also increases. "Long-chain branching (LCB)" can be determined by conventional techniques known in the industry, such as 13C nuclear magnetic resonance (13C NMR) mapping, which is A method such as Randall (Rev. Micromole. Chem. Phys., 1989, C29 (2 & 3), 20 p. 285-297) is used. Two other methods are gel permeation chromatography (GPC-LALLS) coupled to a low angle laser light scattering detector and gel permeation chromatography (GPC-DV) coupled to a differential viscosity detector. The use of these long chain branch detection techniques and their theoretical basis have been stated in the literature. See, for example, 'zimm, BH and Stockmayer, WH, J. Chem. Phys., 17 '1301 (1949) 36 200911847 and Rudin, A., Modern Methods of Polymer Characterization, John Wiley & Sons, New York (1991) pp 103-112. In contrast to "substantially linear ethylene polymer", "linear ethylene polymer" means that the polymer lacks long-chain branches that are measurable or can be represented, that is, the 5 polymers are less than 0.01 long chains per 1000 carbons on average. The branch replaces it. The homogeneous branched ethylene polymer useful in the present invention preferably has a single smelting peak, as measured using a differential broom calorimeter (DSC), as opposed to a heterogeneous branched linear ethylene polymer having at least two melting peaks. Wide branch distribution of heterogeneous branched polymers. 10 Homogeneous branched linear ethylene heterogeneous copolymer is a polymer known to have a linear polymer chain with no measurable long chain branching and a narrow molecular weight distribution. The polymer is a heteropolymer of ethylene and an alpha-olefin comonomer of at least 3 to 20 carbon atoms, and is preferably a copolymer of ethylene and a C3-C10 a-olefin' and more preferably ethylene and propylene. a copolymer of 1-butene, 1-pentene, 1-hexene, heptane or octene, and even more preferably ethylene and propylene, 1-butene, 1-hexene or 1-octene Copolymer. Such a polymer is disclosed, for example, in U.S. Patent No. 3,645,992 to Elston, and a subsequent process using a gold olefin catalyst has been developed to produce the polymer, as shown, for example, in EP 〇 129 368, EP 0 260 999, US Patent No. U.S. Patent No. 4,937,301; U.S. Patent No. 4,935,397; U.S. Patent No. 5, the entire disclosure of which is incorporated herein by reference. This polymer can be produced by conventional polymerization methods (e.g., 'gas phase, paste, solution, and high pressure). In the preferred embodiment of the invention, the vinyl-based heteropolymer is used as a base polymer in the reaction of 37 200911847. In still another embodiment, the vinyl heteropolymer is an ethylene/α-olefin heteropolymer comprising at least one alpha-dilute hydrocarbon. In another embodiment, the heteropolymer further comprises at least one diene. In one embodiment, the ethylene/α-olefin heteropolymer has a molecular weight distribution (Mw/Mn) of less than or equal to 10, and preferably less than or equal to 5. More preferably, the ethylene/α-olefin heteropolymer has a molecular weight distribution of from 1.1 to 5, and more preferably from about 1.5 to 4, or from 1.5 to 3. All individual values and sub-ranges from about 1 to 5 are included and disclosed in this specification. In still another embodiment, the ethylene/α-olefin heteropolymer is a homogeneous branched linear ethylene/α-olefin 10 heteropolymer or a homogeneous branched substantially linear ethylene/α-olefin heteropolymer. Comonomers include, but are not limited to, propylene, isobutylene, 1-butene, 1-pentene, 1-hexene, 3-methyl-1-pentene, 4-methyl-1-pentene, and 1- Octene, non-conjugated diene, polyolefin, butadiene, isoprene, pentadiene, hexadiene (eg 1,4-hexadiene), octadiene, styrene, halogenated - Substituted styrene, 15 alkyl-substituted styrene, tetrafluoroethylene, vinylbenzocyclobutene, naphthalene' cycloolefin (e.g., cyclopentene, cyclohexene, cyclooctene), and mixtures thereof. Basically and preferably, ethylene is copolymerized with at least one C3-C2? alpha-olefin. Preferred comonomers include propylene 1-butene, 1-pentene, 1-hexene, 1-heptene and 1-octene, and more preferably propylene, 1-butene, 1-hexene and - octene. 20 exemplified α-dilute hydrocarbons include propionium, 1-butane, 1-pentene, 1-hexene, 4-methyl-1-pentene, 1-heptene, 1-octene, 1-decene And 1-decene. This α-olefin is expected to be a C3-C10 α-olefin. Preferably, the α-olefin is propylene, 1-butene, 1-hexene or 1-octene. The heterogeneous copolymers described include ethylene/propylene (ruthenium) copolymers, ethylene/butylene (ruthenium) copolymers, ethylene/hexene (ruthenium) copolymers, B38 200911847 olefin/octene (EO) copolymer, ethylene/ A heterogeneous copolymer of α-olefin/diene modified (EA〇DM) such as an ethylene/propylene/diene modified heteropolymer and an ethylene/propylene/octene tripolymer. Preferred copolymers include Ep, EB, £11 and E〇 polymers. 5 Suitable diene and triene comonomers include 7-methyl-1,6-octadiene; 3,7-methyl-1,6-octadiene; 5,7-dimethyl-1 ,6-octadiene; 3,7,11-trimethyl-1,6,10-octanetriene; 6-methyl-i,5-heptadiene; 13-butadiene; l6_heptane丨,7·octadiene; 1,8-decadiene; 1,9-decadiene; 1,10-undecyl-diluted, norbornene; tetracyclododecene; or a mixture thereof And 10 is butadiene; hexadiene; and octadiene; and most preferably 14-hexadiene; hydrazine, 9-decadiene; 4-methyl-1,4-hexadiene; 5_ mercapto·14-hexadiene; dicyclopentadiene; and 5-ethylidene-2-norbornene (ENB). Additional unsaturated comonomers include 1,3-butadiene, quinone-pentadiene, bicyclohexadiene, and dicyclopentadiene; C8-40 vinyl aromatic compound 15 which includes styrene , 〇-, m- and p-mercaptostyrene, diethylbenzene, ethylene diphenyl, vinyl naphthalene; and halogen-substituted C8-40 vinyl aromatic compounds such as chlorostyrene and fluorostyrene. In another embodiment, the ethylene/(X-olefin heteropolymer has a melt index (12) from 0. 01 g/U) minutes to 1500 8/10 minutes, preferably from 01 2 g/1 〇 minutes to 10 〇〇 gA 〇 minutes, and more preferably from 0.5 g / l 〇 minutes to 500 g / 1 〇 knife know ' or from 1 g / ΙΟ minutes to l 〇〇 g / l 〇 minutes, such as using ASTM D 1238 (l9 〇 C ' 2.16 kg load) was measured. All individual values and sub-ranges from 0.01 g/i〇 minutes to 1500 g/l〇 minutes are included and disclosed in this specification. In another embodiment, the ethylene olefin dissimilar copolymer is less than or 39 200911847 equal to a percentage percent crystallinity of 60 乂 比, preferably less than or equal to % percent ' and more preferably less than or equal to 40 percent , as measured by DSC. Preferably, such polymers have a percent crystallinity ranging from 2 percent to 6 Q percent, which includes all individual values and sub-ranges from 2 percent to 60 percent. The individual values and ranges are disclosed in the present specification. In an alternative embodiment, the ethylene/α-olefin heteropolymer has a density of less than or equal to 0.93 g/cc, preferably less than or equal to 〇92_. And more preferably less than or equal to 〇_91 g/cc. In another embodiment, the ethylene/α-olefin heteropolymer has a density greater than or equal to 〇85 g/cc, preferably 10 is greater than or equal to 868.868/(^, and more preferably greater than or equal to 〇87§/(^. In another embodiment, the ethylene/α-olefin heteropolymer has a density of from 0.85 g/cm 3 to 0.93 g/cm 3 and preferably from 0.86 g/cm 3 to 0.92 g / Cm3' and more preferably 〇87 g/cm3 to 0.91 g/cm3. All individual values and sub-ranges from 0.85 g/cm3 to 0.93 g/cm3 are included and disclosed in the 15 specification. The ethylene/α-olefin heteropolymer has a PRR of greater than or equal to 4, preferably greater than or equal to 8, as described below. The viscosity of the heteropolymer is suitably poise (dyne-second/cm 2 ( D-sec/cm2)) in units of 20 shear rate in the range of 0.1-100 radians per second (rad/sec) at 190T: using a dynamic mechanical spectrometer under nitrogen atmosphere (eg Rheometrics RMS-800) Or ARES), measured at a dynamic bending flow of 0.1 to 100 rad/sec. The viscosity at 〇·1 rad/sec and 100 rad/sec can be expressed as ' The ratio of binary values is RR and is expressed as Voj/Vw. 200911847 The PRR value is calculated by the following equation: PRR = RR + [3.82 Heterogeneous Copolymer Mooney viscosity (ML1+4 at 125°C)]x〇. 3. The PRR is determined in accordance with the teachings of U.S. Patent No. 6,680,361, the entire disclosure of which is incorporated herein by reference. Or from 4 to 70. In another embodiment, the ethylene/α-olefin heteropolymer has a PRR of from 4 to 70, or from 8 to 70. In another embodiment, (the ethylene olefin heteropolymer) Having a PRR of from 12 to 60, preferably from 10 15 to 55 ' and more preferably from 18 to 50. Commercially available ethylene/α-olefin heteropolymers having a typical amount of LCB have substantially a pr value of less than three. In another embodiment, the ethylene/α-olefin heteropolymer has a PRR of less than 3, and preferably less than 2. In another embodiment, the ethylene/α-olefin heteropolymer has The PRR of -1 to 3 is preferably from 0.5 to 3' and more preferably from 1 to 3. All individual values and sub-ranges of the PRR values from -1 to 70 are included The τ_-type branch can be copolymerized substantially under the conditions of a suitable reactor under the presence of a geometrically restricted catalyst in the presence of ethylene or other alpha-dilute hydrocarbons with chain-unsaturated macromonomers. Acquired, as described in WO 00/26268, and in the U.S. Patent No. 6,680,361, the entire disclosure of which is incorporated herein by reference. As discussed in WO 00/26268, 'when the amount of Τ-type branches is increased, the efficiency or throughput of the manufacturing process is significantly reduced' until it is economically infeasible to achieve production. The Τ-type LCB polymer can be prepared from a gold olefin catalyst, without an unmeasurable gel, but with a very high amount of Τ-type LCB. Because of the incorporation of the growing aggregate 41 200911847 The macromonomer of the chain has only one reactive unsaturated position, and the resulting polymer contains only side chains of different lengths and is at different intervals in the polymer chain. The H-type branch is basically obtained by the action of copolymerization of ethylene or other alpha olefin with a diene having a double bond in a polymerization process by a non-gold-ene type catalyst. As the name implies, the dilute bridges via a diene to bond a polymer molecule to a different polymer molecule, and the resulting polymer molecule recombines a "Η" which can be described as being more than a long chain branch. Joint state. When a particularly high amount of branches is expected, a Η-type branch is basically used. If too much diene is used, the polymer molecules form too many branches or crosslinks, causing the polymer 10 molecules to become insoluble in the reaction solvent (in the solution process), and thus, causing the polymer molecules to exceed the solution, This results in the formation of gel particles in the polymer. Furthermore, the use of a quinone-type branching agent can deactivate the gold-olefin catalyst and reduce catalyst efficiency. Therefore, when a ruthenium-type branching agent is used, the catalyst used is substantially not a gold-based catalyst. The catalyst used to prepare the bismuth-type branched polymer in U.S. Patent No. 6,372,847 is a vanadium type catalyst. The Τ-type LCB polymer is disclosed in U.S. Patent No. 5,272,236, wherein the amount of LCB is from 0.01 LCB/1000 carbon atoms to 3 LCB/1000 carbon atoms, and wherein the catalyst is a geometrically constrained catalyst. According to P. Doerpinghaus and 20 D. Baird, in The Journal of Rheology, 47(3), pp 717-736 May/June 2003, "Separating the Effects of Sparse Long-Chain Branching on Rheology from Those Due to Molecular Weight in Polyethylenes The free radical process, such as those used to make low density polyethylene (LDPE), produces a polymer 42 with a particularly high amount of LCB 200911847. For example, 'Resin NA952, in Table 1 of the Doerpinghaus and Baird literature, is a LDPE prepared by a free radical process and contains 3.9 LCB/1000 carbon atoms according to Table II. The ethylene alpha olefin (ethylene-octene total 5 polymer) obtained by the Dow Chemical Company (Midland, Michigan, USA), which is considered to have an average amount of LCB, includes the resin Affinity PL1880 shown in Tables I and II, respectively. And Affinity PL1840, which contains 0.018 and 0.057 LCB/1000 carbon atoms, respectively. In one embodiment of the invention, the ethylene/α-anthracene component has a D-type LCB amount that greatly exceeds the currently commercially available ethylene/α-olefin. Table 1 is a list of various types of LCB 10 amounts of ethylene/α-olefin heteropolymers useful in the present invention. In another embodiment, the ethylene/(X-olefin heteropolymer has a PRR greater than or equal to 4. In another embodiment, the ethylene/α-olefin heteropolymer has a PRR greater than or equal to 4, preferably Is greater than or equal to 8, and a molecular weight distribution (MWD) is from 1_1 to 5, preferably from 1.5 to 4 5 ', more preferably from 8 to 38 and most preferably from 2.0 to 3.4. From u to 5 Both individual values and sub-ranges are included and disclosed herein. In yet another embodiment, the ethylene/[alpha]-different hydrocarbon heteropolymer has a density of less than or equal to 0.93 g/cc, preferably less than or equal to 〇. 92 g/cc' and more preferably less than or equal to 0.91 g/cc. In another embodiment, the ethylene/α-olefin heteropolymer is greater than or equal to 〇86 g/cc, preferably 20 is greater than Or equal to 〇_87 g/cc, and more preferably greater than or equal to 0.88 g/cc. In another embodiment, the ethylene/α-olefin heteropolymer has a 〇86 g/cc to 〇.93 g/cc ^;, degrees, and all individual values and sub-ranges from 〇.86§/(^ to 〇.93§/(^ are included and disclosed herein. In another embodiment, this ethylene/α-olefin Xenogeneic copolymerization Having - 43 200911847 PRR greater than or equal to 4, preferably greater than or equal to 8, and a melt index I greater than or equal to 0.1 g / ΙΟ minutes, preferably greater than or equal to 〇 5 g / 1 〇 minutes, or greater than or Is equal to 1.0 g / ΐ ο minutes. In another embodiment, the ethylene/α-olefin heteropolymer has a melting index of less than or equal to 3 〇 g / 1 〇 minutes of 5, preferably less than or equal to 25 g/l〇 min, and more preferably less than or equal to 20 g/ΙΟ min. In another embodiment, the ethylene/(χ-olefin heteropolymer has a 〇_1 g/ΙΟ minute to 30 The melt index of g/l 〇 minute is preferably from 0.1 g/ΙΟ min to 20 g/ΙΟ min, and more preferably from 〇g/1 min to 15 g/ΙΟ min. All individual values 10 and sub-ranges from /i〇 to 3〇g/10 minutes are included and disclosed herein. Ethylene/α-olefin heteropolymers suitable for the present invention can be described in U.S. Patent No. 6,680,361 (also Manufactured by the method of WO 00/26268). Representative examples of suitable heteropolymers are shown in Table 1 below. ΕΑΟ-1, ΕΑΟ-2-1, ΕΑΟ -8 and ΕΑΟ-9 are prepared by the method described in WO 00/26268, which uses a mixed catalyst system described in U.S. Patent No. 6,369,176, the entire disclosure of which is incorporated herein by reference. -1 is prepared by the two-reactor method described in WO 00/26268. It is prepared by the methods described in U.S. Patent Nos. 5,272,236 and 5,278,272. U.S. Patent Nos. 5,272,236; 5,278,272; 6,680,361; and 6,369,176 are incorporated herein by reference. 44 200911847 Table 1A: Ethylene/α-olefin heteropolymer EAO Mooney viscosity MLRA/MV PRR Comonomer ethylene wt% Density g/cc T-branch (low amount) EAO-A 26.2 0.3 -2.9 Butene EAO-B 48.6 1.2 -5.5 Butene T-branches (low to commercial) EAO-C 21.5 0.8 0.6 Octene EAO-D 34.4 1.2 -0.8 Sinan EAO-E 34.1 1.2 -0.5 Octene EAO-EA 32 0 Octene 58 0.86 EAO-F 18.3 0.6 -0.5 Butene T-branch (measured) EAO-1 40.1 3.8 29 Butene 87 0.90 EAO-2 27 2.8 22 Butene EAO-2-1 26 19 Butene 87 0.90 EAO-3 36.8 2.4 15 Butene EAO-4 17.8 2.3 12 Butene EAO-5 15.7 2.0 10 Butene EAO-6 37.1 7.6 70 Propylene EAO-7 17.4 3.4 26 69.5wt% Ethylene / 30wt% propylene / 〇.5% ENB 69.5 EAO -7-1 20 21 Propylene/diene 69.5 0.87 EAO-8 26 45 Propylene 70 0.87 EAO-9 30 17 Octene 70 0.88 H-branch EAO-G 24.5 10.9 76.8 wt% Ethylene / 22.3 wt% C ▲ /0.9 %ENB EAO-H 27 7.1 72 72wt% Ethylene / 22wt% C 4 /6% Hexadiene EAO-I 50.4 7.1 71wt% B & /23wt% C / /6% Hexadiene EAO-J 62.6 8.1 55 71 wt% B; ^ / 23 wt% C _ / 6% hexadiene Mooney viscosity: ML1 + 4 45 at 115 ° C 200911847 A vinyl polymer may be a combination of at least two embodiments disclosed herein. The one ethylene/α-dilute hydrocarbon heteropolymer can be a combination of at least two embodiments disclosed herein. Ii) propylene-based polymer for functionalized olefin-based polymer Suitable propylene-based heteropolymers include propylene homopolymer, propylene heteropolymer, and polypropylene (RCPP) reaction copolymer, which contain about i Up to about 20 weight percent ethylene or an alpha-olefin comonomer of 4 to 20 carbon atoms. The propylene heteropolymer may be a random or block copolymer or a propylene-based tripolymer.

1U 15 20 comonomer suitable for polymerization with propylene includes ethylene, cerium-butene, decylpentene, 1-hexene, 1-heptene, 1-octene, decene, decene, fluorene _ undecene, 1-dodecene, and 4-methyl-pentene, 4-methyl-hexene, 5-methyl small hexene vinyl hexanone, and styrene. Preferred comonomers include ethylene '1' butadiene, 1-hexaped, and U-sweet, and more preferably ethylene. Alternatively, the propylene-based polymer comprises a single unit having a double bond, preferably a di- or triene. Suitable diene and tri-diene comonomers include methyl-1,6-octane dilute; 3,7. dimethyloctane; 5,7-dimethyl

: 辛mu·三%(10)·辛三稀;6m,5-h-绋, 1,3_butadiene; M 1,9-癸 dilute; 11〇_十1 dilute; Norbornene; tetracyclododecene; or a mixture thereof, and preferably more preferably hexamethylene; 1 : dilute, hexamethylene; and octane; and -12-hexa-ene, 4-methyl-1,4-hexadiene; 5-methylol hexyl-ene; dicyclopenta- m, olefin, and 5-ethylidene-2-norbornene (ENB). The unsaturated copolymer of the outer collar, the steroid includes 1,3-pentadiene, dicyclohexadiene 46 200911847 and cyclopentadiene; C8-40 vinyl aromatic compound, including styrene, hydrazine - , m- and p-methylstyrene, diphenyl benzene, ethylene diphenyl, ethylene naphthalene, and halogen-substituted C8-40 vinyl aromatic compounds such as chlorostyrene and fluorostyrene. 5 Particularly advantageous propylene heteropolymers include propylene/ethylene, propylene/;!_butylene propylene/1-hexaped, propylene/4-methyl]-pentanyl, propylene n-octene, propylene/ethylene /1-butene, propylene/ethylene/ENB, propylene/ethylene yi_hexene, propylene/ethylene/1-octene, propylene/styrene propylene/ethylene/styrene. Suitable & t formed is formed by technical methods in this technical field, 10, for example, using a single-site catalyst (goldene or geometric confinement) or ziegler Natta catalyst. The propylene and optional comonomers, such as ethylene or olefin monomers, are polymerized under the technical conditions of the art, for example, as disclosed by Gani et al.

Angew· Macromol. Chem., Vol. 120, 73 (1984), or by E.P. Moore et al., Polypropylene Handbook, published by the University of New York, 15 Hanser Publishing Company, 1996, especially page ii_98. Polypropylene polymers include Shell's KF 6100 homopolymer polypropylene; Solvay's KS 4005 polypropylene copolymer; Solvay's KS 300 polypropylene triacrylate; and INSPIRETM polymer and VERSIFYTM polymer, all available from The Dow Chemical Company. Preferably, the propylene-based polymer has a melt flow rate (MFR) in the range of from 0.01 to 2000 g/10 minutes, preferably from 0.1 to 1 〇〇〇g/l 〇 minutes, and More preferably, it is in the range of 0.5 to 500 g/10 minutes, and even more preferably in the range of 1 to 100 g/10 minutes, as measured according to ASTM D 1238 at 230 ° C / 2.16 kg. 47 200911847 In another embodiment, the propylene/α-olefin heteropolymer has a smelting flow rate (MFR) in the range of up to gram/10 minutes, preferably in the range of 0_1 to 200 g/1 G minutes. More preferably, it is a G 5 to gram old minute range gate or a range of 1 to 50 gram 80 minutes, as measured by ASTM D 1238 at 230 5 C/2.16 kg. All individual values and ranges of persons from 1 to 3 gram / 1 minute are included and disclosed herein. The propylene-based polymer used in the present invention may have any molecular weight distribution (MWD). The wide or narrow MWD propylene-based polymer is formed by the technical methods of this art. The propylene-based polymer having a narrow MWD is advantageously provided by reducing the viscosity or by using a single-site catalyst for the production of a reactor stage (non-reduced viscosity), or by both methods. The propylene-based polymer can be reactor-grade, reduced in viscosity, branched or coupled to provide increased nucleation and rate of crystallization. As used herein, the term "coupled," refers to a rheology-modification of a propylene polymer, so it exhibits a change in resistance to the flow of the melted polymer during extrusion (eg, in the extruder) Before the annular die), therefore, "reducing the viscosity, in the direction of the chain break, "contracting, in the direction of cross-linking or network. For example, coupling" can be added - coupling agent (for example, azide compound ) to a relatively high melt flow rate polypropylene polymer such that the resulting polypropylene polymer composition after extrusion can yield a substantially lower melt flow rate than the initial melt flow rate of 20. Preferably, for coupling or branching The ratio of the subsequent MFR to the initial MFR of the polypropylene is less than or equal to 〇.7:1, more preferably less than or equal to 0.2: 1. A branched propylene-based polymer suitable for use in the present invention is commercially available. For example, Montell North America, trade name profax 48 200911847 PF-611 and PF-814. Or 'suitable branched or coupled propylene-based polymers can be prepared by techniques in the art, such as by peroxide or electron Beam processing U.S. Patent No. 5,414,027 to DeNicola et al. (Using Southern Energy (Ionized) Light Shots with Reduced Oxygen Perimeter); Himont's EP 0 5 190 889 (Electron Beam Radiation of Same Row Polypropylene at Lower Temperatures); US Patent No. 5,464,907 (Akzo Nobel NV); Solvay, EP 0 754 711 (peroxide treatment); and U.S. Patent Application Serial No. 09/133,576 (Azide coupling agent), filed on August 13, 1998. The full text of each of these patents/applications is incorporated herein by reference. 10 Other suitable propylene-based polymers include VERSIFYTM Polymer (The Dow Chemical Company) and VISTAMAXXTM Polymer (ExxonMobil Chemical), LICOCENE TM polymer (Clariant), EASTOFLEXTM polymer (Eastman Chemical), REXTACTM polymer (Hunstman), and VESTOPLASTTM polymer (Degussa 15). Other suitable polymers include propylene-(X- Olefin block copolymers and heteropolymers, and other propylene-based block copolymers and heteropolymers known in the art. In one embodiment, the functionalized propylene-based polymerization Formed from a coupled propylene-based polymer, and preferably an azid-coupled propylene homopolymer. 20 In yet another embodiment, the azide-coupled propylene homopolymer has a propylene polymer of from 1 to 100 g/ The melt flow rate (MFR) of 10 minutes is preferably from 10 to 50 g/ΐ ο, and more preferably from 20 to 40 g/10 min (ASTM D 1238 at 230 ° C / 2.26 kg). In another embodiment, the functionalized propylene-based polymer is a functionalized 49 having a melt flow rate (MFR) of from 50 to 500 g/10 minutes. 200911847 propylene homopolymer is preferably from 8 to 45 〇g/1〇 minutes (ASTM D 1238 at 230 ° C / 2.26 kg conditions). In a preferred embodiment of the invention, a propylene heteropolymer is used as the base polymer in the grafting reaction. In still another embodiment, the propylene-based heteropolymer is a propylene/α-olefin heteropolymer comprising at least one α-olefin. In another embodiment, the heteropolymer further comprises at least one diene. In another embodiment, the propylene-based heterogeneous copolymer is a propylene/ethylene heterogeneous copolymer. Preferred comonomers include, but are not limited to, ethylene, isobutylene, hydrazine-butene, 1-pentene, 1-hexene, 3-methyl-1-pentene, 4-methyl-hydrazine pentoxide, ^ Octene, non-conjugated diene, polyolefin, butadiene, isoprene, pentadiene, hexadiene (eg 1,4-hexadiene), octadiene, styrene, _ Substituted styrene, alkyl-substituted styrene, tetrafluoroethylene, vinylbenzocyclobutene, cyclic hydrocarbon, cycloolefin (eg cyclopentene, cyclohexene, cyclooctene), and the like 15 mixture. Substantially and preferably, the comonomer is a ~ethylene or C4_C alpha olefin. Preferred comonomers include ethylene '1-butene, hydrazine-pentane, hydrazine-hexene, 1-heptene and 1-octene, and more preferably ethylene, hydrazine-butene, hexene and Octene. In another embodiment, the propylene-based polymer is a propylene/alpha olefin iso 20 copolymer having a molecular weight distribution of less than or equal to 5, and preferably less than or equal to 4, and more preferably Less than or equal to 3. More preferably, the propylene-smoke heteropolymer has a molecular weight distribution of from 丄, and preferably to Μ' and more preferably from 2 to 4. In another embodiment, the molecular weight distribution is less than 3.5, and the car balance is preferably less than 3 Torr, more preferably less than 2, more preferably less than 2 hong 50 200911847 and most preferably less than 2.3. All of the values and sub-ranges from 1 to 5 are included in this document and are disclosed herein. In another embodiment, the propylene/alpha-olefin heteropolymer has a melt flow rate (MFR) of less than or equal to 2000 g/min, preferably less than or equal to 5 g/min, and more Preferably, it is less than or equal to 500 g/min, and most preferably less than or equal to 100 g/min, measured by ASTM D 1238 at 230 ° C / 2.16 kg. In another embodiment, the propylene/α-olefin heteropolymer has a melt flow rate (MFR) greater than or equal to 0.01 g/l〇, preferably greater than or equal to 0.1 g/ΙΟ min, more preferably greater than or equal to 5.5 g/l 〇 10 minutes, or greater than or equal to 1 g/10 minutes, measured according to ASTM D 1238 at 230 °C / 2.16 kg. In another embodiment, the propylene/α-different hydrocarbon heteropolymer has a melt flow rate (mfr) ranging from 0.01 to 2000 g/10 min, preferably between 0.1 and 1000 g/10 min. More preferably, it is measured from 〇5 to 5 〇〇g/1〇15, or from 1 to 100g/10分钟's range according to ASTM D 1238 at 230°C/2.16 kg. This document includes and discloses all individual values and sub-ranges from 〇〇1 to 2000 g/10 minutes. In another embodiment, the propylene/alpha olefin heteropolymer has a percent crystallinity of less than or equal to 50 percent, preferably less than or equal to 4 〇 20 percent, and more preferably less than or equal to 35 percent. Percentage, which is measured by DSC. Preferably, such polymers have a percentage of from 2% to 5% of the 结b degree' which includes all individual values and sub-ranges from 2% to 5%. This article discloses the individual values and sub-ranges. In another embodiment, the propylene/α__olefin heteropolymer has a density of 51 200911847 Z equal to 〇.9 Gg/ee, preferably less than or equal to (iv) _, and = less than or equal to C. In another embodiment, the propylene/α· dilute, and the copolymer has a density greater than or equal to 83.83 g/cc, preferably large; or more preferably 0.84 g/cc, more preferably Is greater than or equal to 〇85_. In another embodiment, the propylene/α__ heteropolymer has a density of from 0.83 gW to 0.99 g/cm3, and preferably from 〇84 gw to 〇89' and more preferably from 〇.85. g/cm^〇88 gW. All of the values and sub-ranges from 0.83 g/cm3 to 〇.9〇 gW are included and disclosed herein. 10 15 In another embodiment, the propylene polymer is a propylene/ethylene sieving copolymer having a good amount distribution less than a scale of 5 and a touch of less than or equal to 4, and more preferably Is less than or equal to 3. Preferably, the propylene/ethylidene copolymer has a molecular weight distribution of from 1.1 to 5, and more preferably from 15 to 5, and still more preferably from 2 to 4. In other embodiments, the molecular weight distribution is less than about 3.5, preferably less than 3.0, more preferably less than 2, more preferably less than 2 5 , and most preferably less than 2.3. This document includes and discloses various values and sub-ranges from 丨 to 5. In another embodiment, the propylene/ethylene heteropolymer has a melt flow rate (mfr) of less than or equal to 2000 g/l min, preferably less than or equal to 1000 g/min, and more preferably Less than or equal to 5 〇〇g / 1 〇 minutes, and more preferably 20 is less than or equal to 100 g/10 minutes, which is measured at 230 ° C / 2.16 kg according to ASTM D 1238. In another embodiment, the propylene/α-olefin heteropolymer has a melt flow rate (MFR) greater than or equal to 0.01 g/ΙΟ minutes, preferably greater than or equal to 0_1 g/ΙΟ minutes, more preferably greater than or equal to 0.5 g / i 〇 minutes, or greater than or equal to 1 g / l 〇 minutes ' as per ASTM D 1238 at 230 52 200911847. (:/2·16 kg measurement. In another embodiment, the propylene/ethylene heteropolymer has a melt flow rate (MFR) ranging from 0.01 to 2000 g/1 〇 minute, preferably from 0.1 to 1 〇〇. Between the range of 10 grams per minute, more preferably from 0.5 to 500 grams per 10 minutes, ranging from 5 to ' or from 1 to 100 grams per 1 minute, as measured by ASTM D 1238 at 230 ° C / 2.16 kg. All of the values and subranges from 0.01 to 2000 g/10 minutes are included and disclosed herein. In another embodiment, the propylene/ethylene heteropolymer has a range of from 1 to 300 g/10 minutes. The melt flow rate (MFR) is preferably in the range of 0.1 to 10 200 g/10 min, more preferably in the range of 〇·5 to 1 g/1 〇 minutes or from 1 to 50 g/10 minutes. Between the ranges, as measured by ASTM D 1238 at 230 ° C/2" 6 kg. The various values and sub-ranges from 0 〇 to 3 〇〇 0 minutes are included herein and disclosed herein. In another embodiment Wherein the propylene/ethylene heteropolymer has a percent crystallinity of less than 15 or equal to 50 percent, preferably less than or equal to 40 percent' and more preferably less Or equal to 35 percent, as measured by DSC. Preferably, such polymers have a percent crystallinity ranging from 2 percent to 5 percent, including all individual values and sub-ranges ranging from 2 percent to 5 percent. Individual values and sub-ranges. 20 In another embodiment 'this propylene/ethylene heteropolymer has a density of less than or equal to 0.90 g/cc, preferably less than or equal to 〇·89 g/cc, more Preferably, it is less than or equal to 0.88 g/cc. In another embodiment, the propylene/α-smoke heteropolymer has a density greater than or equal to 〇83 g/cc, preferably greater than or equal to 0.84 g/cc. And more preferably greater than or equal to 〇85 _. 53 200911847 In another "'real_' this propylene/ethylidene copolymer has a density from 0.83 g/cm3 to 0.90 gW, and is preferably 〇84 g/cm3 to 〇89 gW 'more preferably 〇.85 gW to screening gW. This article includes and discloses the individual values and sub-ranges of all hunger 83 gW hunger 9G. 10 15 20 Jj; 匕 归 _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ _ Preferably, it is at least about 80 weight percent and more preferably at least about 85 weight percent based on the total weight of the polymerizable monomer. The basic amount of the unit derived from ethylene in the (10)/ethylene copolymer is derived from ethylene. The basic amount of the unit is at least about 100 weight percent, k is at least about! weight percent and more preferably at least about 5 weight percent, and the maximum amount of units derived from ethylene in such copolymers is substantially no more than U. About 35 weight percent of the polymer, preferably not more than about the weight percent and more preferably not more than the weight percent (based on the 'polymerizable monomer', 悤 weight) right present - extra unsaturated comonomer derived The unit, at least about 0. 01, based on the total weight of the polymerizable monomer, is at least about 1 weight percent and more preferably at least about 5 weight percent, and is not The maximum amount of saturated comonomer derived units is substantially no more than a 'force 35 weight ratio, preferably * more than about a few percent and more preferably no more than about 20 weight percent. The total amount of the combination of ethylene and any unsaturated comonomer derived from the single 4 is substantially no more than 100% of the weight of the heteropolymer copolymer (based on the total weight of the polymerizable monomer), preferably not more than about 3 〇 by weight' More preferably, it does not exceed about 2% by weight. In another embodiment, the propylene-based polymer comprises propylene and hydrazine or one or more unsaturated comonomers other than ethylene, and substantially comprises a heterogeneous total of 54 200911847 mer (based on the total weight of the polymerizable monomers) At least about 60 weight percent of units derived from propylene, preferably at least about 70 weight percent and more preferably at least about 80 weight percent. The at least one unsaturated comonomer of the heteropolymer is at least about 0.1 weight percent, preferably at least about 1 weight percent, and more preferably 5 is at least about 3 weight percent, and the basic maximum amount of unsaturated comonomer does not exceed The heteropolymer (based on the total weight of the polymerizable monomers) is about 40 weight percent, and preferably does not exceed about 30 weight percent. In one embodiment, the acryl-based polymer is prepared using a metal-center, heteroaryl ligand catalyst in combination with at least one activator, such as 10-aluminoxane. In a particular embodiment, the metal is at least one of ruthenium and osmium. More specifically, in certain embodiments of the catalyst, the use of base metals has been found to be preferred over the wrong metals used in the heteroaryl ligand catalyst. The catalyst in a particular embodiment is a composition comprising a ligand and a metal precursor, and optionally may further comprise an activator, a combination of activators and an activator kit. 15 The catalyst used to make the propylene-based polymer further comprises a catalyst comprising an auxiliary ligand-ruthenium complex, an auxiliary ligand-zirconium complex and an optional activator, which catalyzes polymerization and copolymerization. Reactions, especially monomers with olefins, dienes or other unsaturated compounds. Mismatches and oxime complexes can be used. This metal-ligand complex can be in a neutral or charged state. The ratio of ligand to 20 metal can also vary, and the exact ratio depends on the nature of the ligand and the metal-ligand complex. The metal-ligand complex can be of a different type, such as a monomer, a dimer or a higher grade. Suitable catalyst structures and accompanying ligands are described in U.S. Patent No. 6,919,407, the disclosure of which is incorporated herein by reference. In yet another embodiment, the 55 200911847 propylene-based polymer comprises at least 50 weight percent propylene (based on the total weight of the polymerizable monomers) and at least 5 weight percent ethylene (based on the total weight of the polymerizable monomers) and has At 13C NMR peaks of about 14.6 and 15.7 ppm, this corresponds to a region with a peak and the peak is about equal intensity (see, for example, U.S. Patent No. 6,919,407, col. 12, line 64 to column IS, line 51, It is incorporated into the case as a reference). This propylene-based polymer can be prepared by any conventional process. In one embodiment, the process reagent, ie (i) propyl Kii) ethylene and/or at least - unsaturated comonomer, (ι) catalyst, and (iv) optionally, solvent and / or one The molecular weight regulator (e.g., hydrogen) is fed to a single reactor of any suitable design, such as a stirred tank, circuit or fluid bed. The process reagent is contacted (eg, solution, paste, gas phase, suspension, pressure) in a reaction vessel under appropriate conditions to form the desired polymer, and then the reactor output is recovered for use in a post-reaction process. . All reactor production can be recovered in one recovery (eg in a single or batch reactor), or it can be recovered as an effluent stream, which constitutes only one component of the reaction, essentially a small fraction (eg in In the case of a continuous process, wherein the production stream is flowed from the reactor at the same flow rate as the reagent is added to maintain the polymerization as a steady state condition). "Reactive substance, means the content of the reactor after the polymerization and the subsequent polymerization. The reactants include the reactants, solvents (if any), catalysts and products and by-products. The unreacted monomer and the unreacted monomer can be recycled back to the reaction vessel. Suitable polymerization conditions are described in U.S. Patent No. 6,919, No. 4, No. 41, line 23 to column 45, line 43, For reference, a propylene polymer can be a combination of at least two embodiments disclosed herein. The acrylonitrile-thin smoke heteropolymer can be a combination of at least two embodiments of the invention disclosed herein. The heterogeneous copolymer can be a combination of at least two embodiments disclosed herein. iii) an olefin multi-block heteropolymer 5 for a functionalized olefin-based polymer, a dilute hydrocarbon multi-block heteropolymer, and preferably a copolymer. It can also be used as a base polymer for the functionalized olefin-based polymer as described herein. iv) an olefin-based polymer blend for a functionalized dilute-based polymer, in an embodiment of the invention, Can use at least two officials The blend of energizable olefinic polymers is a functionalized dilute hydrocarbon polymer component, for example, a functionalized vinylic polymer as described herein and a functionalized propylene system as described herein. Blends of Polymers. In another embodiment, blending of at least one functionalized olefin-based polymer as described herein with at least one functionalized propylene hydrocarbon multi-block heteropolymer as described herein can be used. In one embodiment, a functionalized vinyl polymer as described herein can be blended with a functionalized olefin multi-block heteropolymer as described herein. In another embodiment, as herein The described functionalized propylene-based polymer can be blended with a functionalized olefin multi-block heteropolymer as described herein. In another embodiment, a functionalized vinyl-based polymerization 20 as described herein and as herein The functionalized propylene-based polymer described can be blended with a functionalized olefin multi-block heteropolymer as described herein. 3. Grafting agent and initiator for the functionalized olefin-based polymer disclosed herein Olefin polymerization The material may be modified by typical grafting, hydrogenation, amine nitrene insertion, or other functionalization known to those skilled in the art. Preferred functionalization In order to use a grafting reaction based on a basic mechanism, the different graftable species can be grafted onto the & singly or in relatively short grafts. These species include unsaturated molecules, each Containing 5 heteroatoms. These species include, but are not limited to, maleic anhydride, monobutyl maleate, dicyclohexyl maleate, diisobutyl maleate, two eighteen Alkyl maleate, N-phenyl succinimide, succinic anhydride, tetrahydrophthalic anhydride, brominated cis-succinic anhydride, chloro-sulphur anhydride, nadic anhydride ), methyl nadia acid 1 phthalic anhydride, alkenyl succinic anhydride, maleic acid, fumaric acid, diethyl butyl ketone, itaconic acid, itaconic acid , butenoic acid, and each of the cool, imine, salt, and Diels-Alder adducts of such compounds. Such species also include decane compounds. The free-radically graftable species of this Shi Xi Xuan* material can be attached to the polymer either alone or in a relatively short graft. Such species include, but are not limited to, ethylene alkoxy decane, vinyl trimethoxy decane, vinyl triethoxy oxime, ethylene ethoxylate, vinyl triclosan, And equivalents thereof, such materials include, but are not limited to, hydrolyzable groups attached to the stone, such as alkoxy, decyloxy, or halide groups. Such materials also include non-hydrolyzable groups such as alkyl groups and decyloxy groups. Other free radical graftable species can be attached to the polymer either alone or in short to longer grafts. Such species include, but are not limited to, methacrylic acid; acrylic acid; Diels_Aldei^a of acrylic acid; including methyl, ethylbutyl/, butyl, ethylhexyl, undecanoic, octadecyl , 58 200911847 and methylaminoethyl methacrylate; including methyl ethyl, butyl, isobutyl, ethylhexyl, dodecanoyl, octadecyl I and vinyl Acrylic acid; glycidyl methacrylate vinegar, tris/heteromethyl propyl ketone, such as 3 hate (10) oxy) propyl: keto-triethoxy her, methyl propyl sulphate - 4 burn, Methacryloxymethyltriethoxynitrile; 2-isopropenylpyrazole i @ , propylene toluene.t 琳 '本乙稀'a-methyl styrene; E-based 甲本本--虱本乙; Ν _ vinyl pyrrolidone, propylene propylene propylene propylene: r heart preparation # ^ ^ 曰, A 10 soil - pitoxy # burning, methacryloxy - decane and vinyl chloride. Soil-alkoxy can use a mixture of free-graftable species comprising at least one of the foregoing species, as an example of a species of styrene. Le 丨 1 butyl dibasic anhydride and benzophenone / acrylonitrile as a description of the thermal grafting process - the method used for the reaction 15 20 stagnation emulsified reducing radicals & (d) may (4) the occurrence of free radicals, but may also be present at the end of the saturated group (for example, B, +, earth) or an internal unsaturated group at the group / this functionalization includes but is not limited to Hydrogenation, southing (such as chaosing), ozonation, transbasic, deuteration, deuteration, epoxidation and grafting. Any functional group, such as i, amine, decylamine, ester, carboxylic acid, oxime, oxime, etc., or functionalized may be added to the terminal or (iv) unsaturated towel by known chemistry. Saturated compound, such as maleic acid. Other methods of energization include the disclosure of U.S. Patent No. 5,849,828, entitled "Mtalation and Functionalization of Polymer and Copolymer"; No. 5,814,708, entitled "Process for Oxidative Functionalization of Polymer Containing Alkylstyrene"; and No. 5,717,039 The name 5 is "Functionalization of Polymer based on Koch Chemistry and Derivatives Thereof". All of these patents are incorporated herein by reference. There are various types of compounds which can initiate a grafting reaction by decomposition to form a radical - especially It is an azo-containing compound, a mercapto peroxyacid and a peroxy ester, an alkyl hydroperoxide, and a dialkyl and a diindenyl peroxide. It has been revealed that the properties of these compounds and their oximes are References: J. Branderup, E. Immergut 'E. Grulke ' eds · "Pollymer Handbook", Wiley, NY, 1999, published fourth edition, Part η, page i_76). Decomposed by the initiator Preferably, the species is an oxygen radical. The initiator is preferably selected from the group consisting of a carboxyl peroxy ester, a peroxy acetal, and a second. The base peroxide and the dithiol group are 15 oxides. Some of the preferred initiators generally used to modify the structure of the polymer are listed below. The respective chemical structures and theoretical free radicals are also listed below. The theoretical free radical yield is the theoretical number of free radicals produced per mole of initiator. Starting agent name theoretical radical yield initiator structure

Dodecane oxime peroxide 〇 〇 CH3(CH2)10C-〇-〇-C(CH2)10CH:

60 200911847 bis 4-butyl peroxide di-t-pentyl peroxide CH; H3C-C- I CH; CH, H3CH2C-C, 〇~ch3 CH, t-butylperoxybenzoate °'~c-ch2ch3 ch3

I CHS a ·?—CH3 CH, • amyl peroxybenzoate CH I CH, ^h2ch〇

In one embodiment, the invention provides an olefin polymer grafted with cis-succinic acid liver. The graft maleic anhydride olefin heteropolymer may or may not contain small amounts of hydrolyzate and/or other derivatives. In the case of the implementation, the graft maleic anhydride olefin heteropolymer has a molecular weight distribution of from about 丨 to about 7, preferably from 1 to 5 to 6, more preferably from 2 to 5. All of the individual values and sub-ranges from about 1 to 7 are included and disclosed in the present invention. In another embodiment, the grafted butadisulfonic anhydride dilute polymer is 61 200911847 #0.855 g/ccJLO.955 g/cc^^^ , g/cc^.0.90 g/cc' and more preferably All individual values and sub-ranges of c from 0.865 g/cc to 895 895 g/cc 〇〇 84 g/cc to 955 are included and disclosed in the present invention. In another embodiment, the amount 5 of maleic anhydride used in the grafting reaction is less than or equal to 1 phr (per hundred parts by weight of the olefin heteropolymer), preferably less than 5 phr, and More preferably from 〇5 to 1〇phr, and the best is from 〇5 to 5

All individual values and sub-ranges of Php 〇 .05 Phr to 1 包括 coffee are included and disclosed in the present invention. In another embodiment, the amount of the initiator used in the grafting reaction is less than or equal to 1 〇 millimole of radical per 1 gram of fluorene dissimilar copolymer, preferably 100 gram of olefin. The heterogeneous copolymer is less than or equal to 6 millimolar free radicals, and more preferably less than or equal to 3 millimolar free radicals per 100 grams of olefin heteropolymer. All individual values and sub-ranges per gram of olefin heteropolymer from 0 01 millimole to 1 gram of millimolar free radicals are included and disclosed in the present invention. In another embodiment, the maleic anhydride composition grafted onto the polyolefin chain is greater than 〇·〇5 by weight (based on the weight of the dilute hydrocarbon heteropolymer such as titration analysis, FTIR analysis) or any In another embodiment, the amount is greater than 〇25 weight percent, and in still-example t' the amount is greater than 〇.5 weight percent. In the preferred embodiment 20, grafting From 0.5% by weight to 2% by weight of maleic acid. All individual values and sub-ranges greater than 0.05% by weight are within the scope of the invention and are disclosed in the present invention. Maleic anhydride and others Saturated heteroatomic species can be grafted onto the polymer via any conventional method, essentially in the presence of a free radical initiator, such as peroxides and azo compounds, or by ionic free radicals. The initiator is preferably any of a peroxide initiator such as dicumyl peroxide, di-tert-butyl peroxide, t-butyl perbenzoic acid, benzamidine. Oxide, cumene hydrogen peroxide Oxide, t-butyl peroctanoic acid. 5 ester, methyl ethyl ketone peroxide, 2,5-dimethyl-2,5-di(tri-butylperoxy)hexane, 2, 5-dimethyl-2,5-di(t-butylperoxy)-3-hexyne, dodecahydroperoxide, and tert-butylperacetic acid S. The nitrogen compound is 2,2'-azobis(bisisobutyronitrile). The organic initiators can have different reactivity at different temperatures, and can form different types of free 10 groups for grafting. Those skilled in the art can select an appropriate organic initiator according to the needs of the grafting conditions. The amount and form of the initiator used in the grafting process, the amount of maleic anhydride, and the reaction conditions, including degree, Time, shear, environment, additives, diluents, and the like can impact the final 15 structure of the maleic acid polymer, such as maleic anhydride/butadiene anhydride grafted onto the polymer. The amount, its oligomers, and derivatives thereof, including the hydrolysate, are affected by the considerations in the previous section I. In addition, the amount of branching and the amount of cross-linking of the form are also affected by the reaction conditions and concentration. In general, it is preferred to minimize cross-linking during methacrylation. The composition of the base olefin heteropolymer also plays a role in the final structure of the cis- 20 olefinic acid polymer. Will then affect the nature and use of the final product. Basically, the amount of initiator and maleic anhydride used does not exceed the amount required for each of the functionalized polymer and its subsequent use, the amount of which is determined The expected degree of maleic acidation and the expected melt flow. 63 200911847 The grafting reaction should be based on conditions that maximize grafting to the polymer chain and minimize side reactions that are not grafted to the olefin heteropolymer. The sub-reaction is carried out as a homopolymerization of a grafting agent. It is rare that some components of bismuth maleate (and/or its derivatives) are not grafted to an olefin heteropolymer, and it is usually expected to be 5 The grafting agent of the reaction can be minimal. The grafting reaction can be carried out in a molten state, a solution state, in a solid state, in a swelling sorrow, and the like. The maleic acid action can be carried out in a multi-unit apparatus such as, but not limited to, a twin screw extruder, a single screw extruder, a Brabenders, a batch reactor, and the like. Preferred cis-succinic anhydride graft polymers include AMPLIFY polymers available from The Dow Chemical Company. Other examples include fusaBOND (available from DuPont), EXXELOR (available from Exx〇nM〇bil), and POLYBOND (available from Chemtura). In one embodiment, the maleic anhydride graft polymer comprises from 0.3 weight percent to 1 to 5 weight percent of the grafted cis-butenedienedic anhydride, based on the total weight of the graft polymer. In still another embodiment, the maleic acid needle graft polymer is a maleic anhydride grafted vinyl polymer. In still another embodiment, the maleic anhydride graft polymer is a maleic anhydride grafted ethylene/〇1_dilute hydrocarbon heteropolymer. Still another embodiment of the present invention provides an olefin heteropolymer copolymerized with other compound-containing compounds. In one embodiment, the grafted olefin heterogeneous copolymers have the same or similar molecular weight distribution and/or density as the grafted maleic anhydride olefin heteropolymer described above. In another embodiment, the branched olefin heteropolymers are prepared using the same or similar amounts of the grafting compound initiator for the grafted cis-butenedihydride olefin heteropolymer. The two grafted dilute soda heteropolymers contain the same or similar amounts of the grafting compound as described above for grafting cis-butane. Other group-containing compounds include, but are not limited to, dibutyl maleic acid vinegar, dicyclohexyl succinimide, diisobutyl cis-butane diacetate, decyl cis-butyric acid g hydrazine, N_phenyl cis-butyl diimide, barkang anhydride, four-nine gorge, indimethacin needle, nadic needle, methyl nadic anhydride, dilute dicetic acid needle, cis-butyl Dicarboxylic acid, anti-butene-hub, ethyl-trans-butadienoate, itaconic acid, syconic acid, baronic acid, and the like, the imine thereof, and the like, and Its Diels-Alder adduct. Still another embodiment of the present invention provides an olefin heteropolymer grafted with other carbonyl-containing compounds. In one embodiment, the grafted olefin heterogeneous copolymers have the same or similar molecular weight distribution and/or density of the grafted maleic anhydride dilute hydrocarbon heteropolymer. In another embodiment, in the alternative embodiment, the grafted olefin dissimilar copolymers are initiated using the same or similar amounts of the grafting compound for the grafting maleic anhydride olefin heteropolymer. Prepared by the agent. In another embodiment, the grafted olefin heteropolymers contain the same or similar amounts of the grafted compound as described above for grafting maleic anhydride. Other group-containing compounds include, but are not limited to, dibutyl cis-butyrate, dicyclohexyl maleate, diisobutyl maleate, di-octadecyl maleate, N-phenyl maleimide, citraconic anhydride, tetrahydro-imumic anhydride, brominated maleic anhydride, gas-succinic anhydride, nadic anhydride, methyl nadic anhydride, alkenyl Alkenic anhydride, cis-butene 65 200911847 diacid, antibutanic acid, monoethylidene diacid acid, chitosan, citraconic acid, crotonic acid and the like, their imine, Its salt, and its Diels-Alder adduct. In one embodiment, the invention provides an olefin-based heteropolymer grafted with at least one decane compound. The grafted xenon-smoke heterogeneous copolymer may or may not contain small amounts of hydrolysate and/or other derivatives. In another embodiment, the decane-grafted olefin-based heteropolymer has a molecular weight distribution of from about 1 to 7, preferably from 丨5 to 6, and more preferably from 2 to 5. All of the individual values and sub-ranges from about 1 to 7 are included and disclosed in the present invention 10. In another embodiment, the decane-grafted olefin-based heteropolymer has a density from 0.855 g/cc to 0.955 g/cc, preferably from 〇86 g/cc to 〇9 〇g/cc, and more The best is from 0.865 g/cc to 〇_895 g/cc. All individual values and sub-ranges from 〇 84 _ to 5 g/cc are included and disclosed in the present invention. 15 纟 - 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施 实施To 4 coffee. All individual values and sub-ranges from 〇5 coffee to 6 coffee are included and disclosed in the present invention. In another example, the amount of the initiator for the graft reaction towel is less than or equal to 4 millimoles of radical per gram of the olefin heteropolymer, preferably 100 grams of the olefinic heteropolymer. Less than or equal to 2 millimolar free radicals, and more Y soil is less than or equal to 1 millimole of free radical per 1 gram of the dilute hydrocarbon heteropolymer. All individual values and sub-ranges of from 001 millimole to 4 millimole of free radical per 100 grams of hydrocarbon-incorporated copolymer are included and disclosed in the present invention. 66 200911847 In another embodiment, the amount of decane grafted onto the polyolefin chain is greater than or equal to 0.05 weight percent (based on olefin heteropolymer weight) as determined by FTIR analysis or other suitable method. In still another embodiment, the amount is greater than or equal to 0.5 weight percent, and in still another embodiment, the amount of 5 is greater than or equal to the weight percent of h2. In a preferred embodiment, the amount of the decane composition of the graft on the olefin heteropolymer is from 5% by weight to 4.0% by weight. All individual values and sub-ranges greater than 〇〇5 weight percent are within the scope of the invention and are disclosed in the present invention. Suitable decanes include, but are not limited to, those represented by the chemical formula (1): 10 CH2=CR-(COO) X (CnH2n)ySiR3 (1). In the formula, R is a hydrogen atom or a methyl group; x&y is 〇 or 丨, and when X is 1, the 彳 y is 1; n is a one! An integer of up to 12, preferably 丨 to 4, and each R, each independently an organic group, includes but is not limited to an alkoxy group having up to 12 carbon atoms (eg, methoxy, ethoxy) , butoxy), aryl 15 oxy (eg phenoxy), aralkyloxy (eg abbreviated oxy), aliphatic or aromatic oxaoxy, aromatic oxy, having 丨 to 12 An aliphatic aryloxy group of a carbonaceous material (for example, a methyloxy group, an ethyloxy group, a propyloxy group), an amine group or a substituted amine group (alkylamino group, arylamine group), or one having A lower alkyl group having up to 6 carbon atoms. In one embodiment, the decane compound is selected from the group consisting of vinyl trialkoxy decane, vinyl tridecyloxydecane or vinyl trioxane. In addition, any decane or decane mixture which is effective for grafting and/or crosslinking to the olefin heteropolymer can be used in the practice of the invention. Suitable decanes include unsaturated <6<6><6>, wherein the unsaturated unsaturated smoky group, 67 200911847, such as vinyl, propyl, isopropenyl, butyryl , cyclohexene or γ-(meth) propylene oxyallyl, and a hydrolyzable group such as a monohydrocarbyloxy group, a benzyloxy group, or a transaminyl group, or a compound. Examples of hydrolyzable include methoxy, ethoxy, decyloxy, ethoxylated, propyloxy, chloro, and pendant or 5-arylamine groups. 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 。 And the text case is used as a reference. Preferably, the stone sizzling comprises ethylene trimethoxy sulphate, ethylene triethoxy sulphur, and tris (trimethoxy sylylene) propyl methacrylate 10 (H methyl) propyl Propyltrimethoxywei), and a mixture of materials. The calcination can be grafted onto the polymer by any conventional means, essentially in the presence of free radicals, such as peroxides and azo compounds, or by ionic free radicals. The organic initiator is preferably a peroxide, such as dicumyl peroxide, di-tert-butyl persulfate, t-butyl perbenzoic acid, benzamidine peroxidation. , cumene peroxide, t-butyl peroctanoic acid, methyl ethyl peroxide, 2,5-dimethyl 2,5-(2-butylperoxy) 2,5-Dimethyl_25_di(third, butyl-peroxy)-3.hexahydrate, dodecaine peroxide, and third.butylperethyl> The suitable azo compound is 2,2,-azo (double isobuty). The use of the surname START agent and Shi Xizhuo will affect the most important, and, and the graft polymer of Shi Xiyuan. The degree of grafting, for example, in the graft polymer and the structure formed in the matured polymer and the degree of iJt will continue to affect the physical and mechanical properties of the final product. Basically, the amount of starter and shixiyuan used does not exceed the amount that determines the amount of (4) expected to be produced and the nature of the polymer. , 68 200911847, the branch reaction should be grafted to the polymer chain" to enlarge and make the non-grafted material small (four) bamboo, the side reaction of the branching agent. Some Wei _ row amount or No homogenization with 'Lingui sand molecular knot, compatibility and / or its 10 15

20 The aging of the stone and the grafting (crosslinking) is promoted by the cross-linking catalyst, and a catalyst which effectively promotes the crosslinking of the specific grafting Wei can be used. These catalysts include acid money, metal compounds for machine machines, titanium titanates, acid salts, and complexes or salts of ships, knots, iron, nickel, zinc and tin. _ can use monobutyl-tin laurate, dioctyltin maleate, dibutyl, tin diacetate, 'dibutyltin dioctoate tin, tin acetate, naphthalic acid, octanoic acid, naphthalene drill and the like By. The amount of employment depends on the specific use (4). * A dual cross-linking system can be effectively used in a particular embodiment of the present month to use a combination of radiation, heat, moisture and crosslinking steps. For example, it is contemplated to use a combination of a peroxide crosslinker and a decane crosslinker, peroxygen; a combination of a ruthenium crosslinker with radiation, or a sulphur crosslinker with a hydroxy crosslinker. The double cross-linking system is disclosed and claimed in U.S. Patent No. 5,911,9, the disclosure of which is incorporated herein by reference. 4_ In-situ Aminetization of Functionalized Olefinic Polymers and In-situ Warp Functionalization In a preferred embodiment of the invention, the functionalized flue-cured polymer is an amine-functionalized A polymer or a hydroxyl group-functionalized olefinic polymer. The process for producing a dilute hydrocarbon polymer which is functionalized by an amine or functionalized can be carried out in a - extrusion/scraper, and (4) acid Xuan Shuzhi 69 200911847 agent can be grafted to the first part of the extruder The olefin-based polymer is then subjected to a sit-in action in the latter order of the second-order diamine form prior to granulation. Alternatively, the two extruders can be operated in series, or the mixing device can be melted to perform the two chemical steps. 5 In order to prepare an amine-functionalized olefin-based polymer from an anhydride-grafted olefin-based polymer in a molten state without a competing crosslinking reaction, it is necessary to use a compound having the formula H2N-R-NH-R" a primary-secondary diamine which is at least a -C2 hydrocarbyl group. A stoichiometric excess or stoichiometric equivalent of a diamine can be used. Suitable for a primary-secondary diamine comprising a compound of the following structure: 10 _ ~R'~ NH—R2 (1) 〇 In structure (I), the core is a divalent hydrocarbon group, and preferably a linear hydrocarbon having the formula -(CH2)n•, wherein n is greater than or equal to 2, and preferably It is preferably 2 to 10', more preferably 2 to 8, and most preferably 2 to 6. & is a monoterpene group containing at least 2 hindering atoms' and may be optionally substituted by a group containing a hetero atom, such as 〇11 Or 15 SH. R2 is preferably a linear dazzle having a chemical formula 3, wherein 1 to 10, and η is preferably from 丨 to 9, more preferably from 丨 to 7, and most preferably from 丨 to 5. ', and · and - monoamines include but are not limited to Ν-ethylethylene diamine, fluorenyl phenylethylene diamine, hydrazine-stupyl-1,2-phenylenediamine, hydrazine- Phenyl-1,4-phenylenediamine and Ν_(2 An example of a preferred one-stage 20-diamine is as follows: N-(ethyl)acetamidinediamine, N-ethyl-1,3-propanediamine, 70 200911847

N-ethyl-1,4-butanediamine, N-(2-transethylethyl)ethylenediamine,

N-(phenyl)ethylenediamine, and N-(2-hydroxypropyl)ethylenediamine. The alkanolamine is a compound containing an amine group and at least a hydroxyl group, preferably having only one hydroxyl group. The amine may be a primary or primary amine, and is preferably a primary amine. The polyamine is a compound containing at least a diamine, preferably a diamine group. Suitable alkanolamines are those having the following structural formula (II):

H2N——R, —OH In the structure (II), R is a divalent hydrocarbon group, and preferably a linear hydrocarbon having the formula -(CH2)n-, wherein η is greater than or equal to 2, and η is more Preferably, it is from 2 to 10, more preferably from 2 to 8, and most preferably from 2 to 6. Other alkanolamines include, but are not limited to, ethanolamine, 2-amino-1-propanol, 3-amino-1-propanol, 2-amino-1-butanol, and 2-aminobenzylmethyl. alcohol. An example of a preferred alkanolamine is as follows. Η2ν 2-Aminoethanol Η2ν/\^^〇Η 3-Aminopropanol /0Η 4-Aminobutanol η2ν

Me 1-Amino-2-3⁄4-propylpropanyl h2n 2-(2-Aminoethoxy)ethanol 71 200911847 Other examples of suitable alkanolamines and suitable diamines are represented by the following structural formula (III): HX-CH-CH-I- °CH2-CH2-NH2

l RRK (HI) 〇 In structure (III), X is O or X = NR' (R' = alkyl); and each R is independently 5, CH3, or CH2CH3; and n is 0 to 50. The disclosure and preparation of hydroxyamines can be found in U.S. Patent Nos. 3,231,619, 4, 612, 335, and 4, 888, 446, the disclosures of which are incorporated herein by reference. Examples of preferred alkanolamines include 2-aminoethanol, 1-amino-2-propanol, 2-amino-1-propanol, 3-amino-1-propanol, 2-(2-amine Ethyl ethoxy) ethanol, 1-amino-2-butanol, 10 2-amino-3-butanol, and polyoxyalkylene glycol amine. A preferred alkanolamine is 2-aminoethanol. In one embodiment, the maleic anhydride olefin-based polymer is functionalized with a primary-secondary diamine or an alkanolamine. In still another embodiment, the maleic anhydride is used in an amount of from 0. 10% by weight to 5.0% by weight, preferably from 0.50% by weight to 3.0% by weight based on the weight of the unfunctionalized grafted olefin polymer. The percentage, and more preferably from 1.0% by weight to 2.0% by weight. In still another embodiment, the peroxide is used in an amount of from 0.01% by weight to 0.5% by weight, preferably from 0.05% by weight to 0.3% by weight, based on the weight of the unfunctionalized grafted hydrocarbon-based polymer, and more preferably It is from 0.1% by weight to 0.2% by weight. In still another embodiment, the amount of the primary-secondary diamine or alkanolamine used is from phase 72 200911847 to 1 to 10 moles of amine for the graft anhydride, preferably from 2 to 8 moles of amine, and more It is preferably from 4 to 6 moles of amine. 5. The original functionalization of a functionalized olefin-based polymer using maleic acid. The 5 hydroxy- and amine-functionalized ethylene-octene copolymer may also be represented by the corresponding cis-butenylene. The peroxide-initiated grafting of an amine acid or a derivative thereof is prepared in a step in which the maleic acid is reacted with maleic anhydride and an alkanolamine or a primary-secondary diamine. And formed. Maleic acid is represented by the following structural formula (IV): Ο

% In the formula (IV), R1 and R2 are each independently hydrogen or a linear or branched C1-C20 hydrocarbon group; R3 is hydrogen or a linear or branched C1-C20 hydrocarbon group; R4 is a linear or Branched hydrocarbyldi-yl; X is OH or NHR5, wherein R5 is a linear or branched hydrocarbyl group, or a monohydroxyethyl group. In a preferred embodiment, R1 and R2 are each independently hydrogen or a C1-C10 hydrocarbon group, more preferably a C1-C8 hydrocarbon group, and more preferably a C1-C6 hydrocarbon group which is linear or branched. In a preferred embodiment, R3 is hydrogen or a C1-C10 hydrocarbon group, preferably a C1-C8 hydrocarbon group, and more preferably a C1-C6 hydrocarbon group, which is linear or branched. In a preferred embodiment, R4 is a C1-C20 hydrocarbon group, preferably a C1-C10 hydrocarbon group, more preferably a 20 C1-C8 hydrocarbon group, and most preferably a C1-C6 hydrocarbon group which is linear or branched. In a preferred embodiment, R5 is a C1-C20 hydrocarbon group, preferably a C1-C10 73 200911847 hydrocarbon group, more preferably a C1-C8 hydrocarbon group, and most preferably a C1-C6 hydrocarbon group which is linear or branched. In another embodiment, R5 is linear -(CH2)n-CH3, wherein η is greater than or equal to 1, and preferably η is from 1 to 9, more preferably from 1 to 7, most preferably from 1 to 5. Other examples of R5 include, but are not limited to, the following structures: -CH3, 5-CH2CH3, -CH2CH2CH3, -CH2CH2CH2CH3, -CH(CH3)CH3, -CH(CH3)CH2CH3, -CH2CH(CH3)CH3, -CH(CH3 CH2CH2CH3, -CH2CH(CH3)CH2CH3 and -CH2CH2CH(CH3)CH3. Other maleic acid structures are as follows. In each structure, 10 R3 and R4 are defined as follows. Ο 〇

Preferably, the maleic acid exhibits the structural formula (V) as shown below: 200911847 This polyolefin is functionalized with a maleic acid as shown by structural formula (v). In one embodiment, the maleic acid is used in an amount of from 0.10 weight percent to 5.0 weight percent, based on the weight of the unfunctionalized graft olefin system, more preferably from 0.50 weight percent to 3.0 weight percent, and more preferably from 5 It is from 1.0% by weight to 2.0% by weight. In still another embodiment, the peroxide is used in an amount of from 0.01% by weight to 1% by weight based on the weight of the unfunctionalized grafted olefin system, preferably from 0.01% by weight to 0.5% by weight, and more preferably 0.05% by weight. The percentage is up to 10 0.3 weight percent, most preferably from 0.1 weight percent to 0.2 weight percent. 6. Diamine Absorption Process for Functionalized Olefinic Polymers The functionalization of olefinic polymers as described herein can also be carried out using a diamine absorption process. Herein, the monoolefin polymer is first functionalized with a group reactive with an amine functional group. Preferably, the olefin-based polymer is functionalized with an anhydride group. The at least one diamine is mixed with the functionalized olefin-based polymer at a temperature lower than the melting point of the olefin-based polymer, and is preferably at room temperature. This diamine is allowed to absorb or inhale the olefin-based polymer and react with the diamine-reactive group to form mono-decanoic acid. The reaction of the diamine with a diamine reactive functional group to form an imine ring can be accomplished by subjecting the mixture to a heat treatment, such as a 20 melt extrusion process. Suitable diamines include those discussed herein. This absorption process helps ensure that the diamine is completely mixed with the olefin-based polymer for an effective functionalization reaction. (VI) ο Suitable for a primary-secondary diamine comprising the following compound of formula (VI): H2N-R, -NH - R2 75 200911847 In the formula (VI), R is a divalent hydrocarbon group, And preferably a linear hydrocarbon of the formula -(CH2)n-, wherein η is greater than or equal to 2, and η is preferably from 2 to 10, more preferably from 2 to 8, and most preferably from 2 to 6. R2 is a monovalent hydrocarbon group containing at least 1 carbon atom, and may be optionally substituted by a group containing a hetero atom such as OH 5 or SH. R2 is preferably a linear hydrocarbon of the formula -(CH2)n-CH3 wherein n is from 0 to 10, and η is preferably from 0 to 9, more preferably from 0 to 7, and most preferably from 0 to 5. 10 Suitable for primary-secondary diamines including but not limited to fluorenyl-mercapto-ethylenediamine, hydrazine-ethylethylenediamine, fluorene-phenylethylenediamine, fluorenyl-fluorenyl-1,3-propane Amine, anthracene-mercapto ethylenediamine, anthracene-phenyl-1,2-phenylenediamine, anthracene-phenyl-1,4-phenylene diamine, 1-(2-aminoethyl) - Sigma, and N-(2-J^i-ethyl)-ethylenediamine. An example of a preferred one-stage diamine is shown below.

NH2, V 'Et N-(ethyl)ethylenediamine,

Ν-ethyl-1,3-propanediamine

ΝΗ2, ν v 'Et N-ethyl-1,4-butanediamine,

Called v v , 〇H N-(2-hydroxyethyl)ethylenediamine, Me

N-(phenyl)ethylenediamine

N-(2-hydroxypropyl)ethylenediamine, ,Me

NH, v 'Me N-(indenyl)ethylenediamine,

NH2·" v 'Me N-methyl-1,4-butanediamine, NH2 Ν-methyl-1,3-propanediamine

.-(2-Aminoethyl) ϋ辰唤76 761111847 . 5 f olefin multi-block heteropolymer olefin multi-block heteropolymer is described on March 17, 2005, filed for international application PCT/US05 US Patent Application No. 2006/0199914, U.S. Provisional Application No. 60/876,287, U.S. Patent Application Serial No. 60/876,287, filed on Mar. U.S. Provisional Application Serial No. 60/553,906, the entire disclosure of which is incorporated herein by reference. In a preferred embodiment, the olefin multi-block heteropolymer is a methene/α-olefin multi-block heteropolymer. In yet another embodiment, the ethylene/(X-olefin multi-block heteropolymer comprises greater than 50 mole percent ethylene (based on total moles of polymerizable monomers). This ethylene/alpha-olefin multi-block heterogeneous The copolymer has at least one of the following characteristics: 15 (1) an average block index greater than 0 and up to about 1.0 and a molecular weight distribution Mw/Mn greater than about 1.3; or / (2) at least one molecular component when using TREF When fractionated, when eluted between 40 ° C and 130 ° C, it is characterized in that the component has a block index of at least 0.5 and up to about 1; or 20 (3) has a Mw of about 1.7 to about 3.5. Mn, at least one is a melting point Tm' of the degree Celsius and a density d of g/cm3, wherein the values of Tm and d correspond to the following relationship: Tm > -2002.9 + 4538.5(d) - 2422.2(d)2, preferably Is >-6553.3+13735(d)-7051.7(d)2; or 77200911847(4)-Mw/Mn of about 1.7 to about 3.5, and characterized by a heat of ray of J/g And ΔΤ in degrees Celsius, which is defined as the temperature difference between the highest DSC peak and the highest CRYSTAF peak, where ΔΤ has the following relationship with the value of AH: 5 pairs ΔΗ greater than 0 and as high as 130 J/g ΔΤ >-0·1299(ΔΗ) + 62.81, for 八11 greater than 130>^, 厶7^48°(:, where the CRYSTAF peak is determined using at least 5 percent polymer accumulation, and if less than 5 percent The polymer has an identifiable CRYSTAF peak, and the CRYSTAF temperature is 30 ° C; or 10 (5) an elastic recovery Re, whereby the compression molded film of the ethylene/α-olefin heteropolymer is at 300% strain and 1 cycle The measured percentage, and the density d' of g/cm3, wherein the values of Re and d satisfy the following relationship when the ethylene/α-olefin heteropolymer is substantially non-crosslinked: Re>148M629(d); 6) - a molecular component which, when eluted between 4 〇 15 ° 〇 and 130 ° 当 when using TREF component, is characterized in that the component has a comparable random ethylene elution at the same temperature The heterogeneous copolymer component is at least 5 percent higher than the molar comonomer content, wherein the comparable random ethylene heteropolymer has the same comonomer and has a melt index, density, and molar content of the monomer (based on the total polymer) is 100% of the 20 kinds of ethylene/α-smoke heterogeneous copolymerization Ratio; or (7) storage modulus at 25 ° C 'G, (25 ° C), and storage modulus '100' at 100 ( (l 〇 (TC), where G, (25 ° c) versus G , (1〇〇 °c) ratio between about 1: : to about 9: 1 range. In a preferred embodiment, the ethylene/α-olefin multi-block heteropolymer 78 200911847 has a melting point Tm of from about 1.7 to about 3.5, at least one degree Celsius in Mw/Mn of property (3), and The density d of g/cm3, where the values of Tm and d correspond to the following relationships:

Tm > -6553.3 + 13735(d) - 7051.7(d)2. In one embodiment, the ethylene/α-olefin multi-block heteropolymer is one of the properties (1) to (7) as discussed above. In another embodiment, the ethylene/α-olefin multi-block heteropolymer has at least the property (1) as discussed above. In another embodiment, the ethylene/α-olefin multi-block heteropolymer has a combination of at least two of the properties (1) to (7) as discussed above. In another embodiment, the ethylene/α-olefin multi-block heteropolymer has at least the properties (1)' as described above and with the properties (2) to (7) as discussed above. At least a combination of the two. In another embodiment, the 'ethylene/α-olefin multi-block heteropolymer is characterized by at least one of the following characteristics: 15 (4) having a Mw/Mn of from about 1.7 to about 3.5, at least one melting point Tm' of degrees Celsius and The density d of g/cm3, where the values of Tm and d correspond to the following relationships:

Tm > -2002.9 + 4538.5(d) - 2422.2(d)2 - preferably 1^6553.3 + 13735(d) - 7051.7(d)2, or -° (b) having Mw/Mn of from about 3.5 to about 3.5 And characterized by a heat of fusion of J/g AH, and a ΔΤ of degrees Celsius, which is defined as the temperature difference between the highest CscSTAF peak of the highest Dsc peak, wherein the values of at and ah have the following relationship: ΔΗ is greater than 0 and up to 13〇J/g, AT > -0.1299(ΔΗ) + 62 8, 79 200911847 For ΔΗ greater than 130 J/g, AT 2 48 °C, where CRYSTAF peak is at least 5 percent polymer accumulation Measured, and if less than 5 percent of the polymer has an identifiable cRYSTAF peak' then the CRYSTAF temperature is 3 (TC; or 5 (c) characterized by an elastic recovery Re, whereby the ethylene/α-olefin heteropolymer The percentage of the compression molded film measured at a 3 〇〇 percent strain and a helium cycle, and the density d of g/cm 3 , wherein when the ethylene/α-olefin heteropolymer is a smectite-free crosslinked phase, The values of Re and d satisfy the following relationship: Re >1481-1629(d); or 10 (d) a molecular component which is eluted between 40 C and 130 C when TREF is used. special The component has a molar comonomer content that is at least 5 percent higher than the comparable random ethylene heteropolymer component eluted at the same temperature, wherein the comparable random ethylene heteropolymer has the same comonomer And having a melt index, density and molar copolymer 15 monomer content (based on the total polymer) within 10% of the ethylene/α-olefin heteropolymer; or (e) characterized by a storage mold at 25 ° C Number, G, (25 ° C), and storage modulus at 10 CTC, G, (100 ° C), where G, (25 ° C) vs. G, (100 t:) ratio is between about 1: 1 to about 10 : 1 range; or 20 (f) at least one molecular component, which is between 40 C and 130 when TREF is used. (: During elution, it is characterized by at least 0.5 and south to about The block index of 1 and the molecular weight distribution Mw/Mn greater than about 1.3, or (g) - the average block index is greater than 〇 and up to about 1 〇 and a Mw/Mn is greater than about 1.3. 200911847 In an embodiment, The ethylene/α-olefin multi-block heteropolymer and having one of the properties (a) to (g) as discussed above. In another embodiment The ethylene/α-olefin multi-block heteropolymer has at least the property (g) as discussed above. In another embodiment, the ethylene/α-olefin multi-block heteropolymer has 5 properties as discussed above. A combination of at least two of (a) to (g). In another embodiment, the ethylene/α-olefin multi-block heteropolymer has at least the properties (g) as discussed above and is combined with at least two of the properties (a) through (f) as discussed above. . In a preferred embodiment, the ethylene Ax-olefin multi-block heteropolymer 10 has a melting point Tm of Mw/Mn of from (1) to about 3.5, at least one degree Celsius, and Is the density d of g/cm3, where the values of Tm and d correspond to the following relationship:

Tm > -6553.3 + 13735(d) - 7051.7(d)2. The ethylene/α-olefin multi-block heteropolymer substantially comprises ethylene and up to 15 copolymerizable α-olefin comonomers in a polymerized form, characterized in that at least two polymerizable monomers having different chemical or physical properties are present. A multi-block or segment of a unit. That is, the ethylene/α-olefin heteropolymer is a block heteropolymer, preferably a multi-block heteropolymer or copolymer. The terms "heteropolymer" and "copolymer" are used interchangeably herein. In certain embodiments, 20 such multi-block copolymers can be represented by the formula: (ΑΒ)η, where η is at least 1, preferably an integer greater than 1, such as 2, 3, 4, 5, 10, 15, 20, 30, 40, 50, 60, 70, 80, 90, 100, or higher, "Α" means a hard block or segment, and "Β" means a soft block or segment. Compared with 81 200911847, this A and B are connected in a substantially linear mode, opposite to the substantive or substantial star pattern. In other embodiments, the A block and the B block are randomly distributed in a long polymer chain. In other words, the block copolymer generally does not have the following structure.

AAA-AA-BBB-BB 5 In yet another embodiment, the block copolymer typically does not have a third type of block comprising different comonomers. In yet another embodiment, each of block A and block B has a monomer or comonomer that is substantially randomly distributed in the block. In other words, neither Block A nor Block B contains sub-segments (or sub-segments) of two or more different compositions, such as an end segment, which has a composition that is different from the rest of the blocks. Things. Multi-block polymers essentially contain varying amounts of "hard" and "soft" segments. By "hard" segment is meant that more than about 95 weight percent ethylene, and preferably greater than about 98 weight percent, is present in the blocks of the polymerized units based on the weight of the polymer. In other words, the comonomer content (non-ethylene monomer 15 content) in the hard segment is less than about 5 weight percent, and preferably less than about 2 weight percent, based on the weight of the polymer. In certain embodiments, the hard segment comprises all or substantially all of the ethylene. In another aspect, a "soft" segment means that greater than about 5 weight percent comonomer content (non-ethylene monomer content), preferably greater than about 8 weights, is present in the blocks of the polymerized units based on the weight of the polymer. Percent, 20 is greater than about 10 weight percent, or greater than about 15 weight percent. In certain embodiments, the comonomer content in the soft segment can be greater than about 20 weight percent, greater than about 25 weight percent, greater than about 30 weight percent, greater than about 35 weight percent, greater than about 40 weight percent, greater than about 45 weight percent, greater than about 50 weight percent, or greater than about 60 weight percent. 82 200911847 The soft segment is present in the block heteropolymer in an amount of from about 1 weight percent to about 99 weight percent, preferably from about 5 weight percent to about 95 weight percent, based on the total weight of the block heteropolymer. From about 1 weight percent to about 90 weight percent, from about 15 weight percent to about 85 weight percent '5 from about 20 weight percent to about 80 weight percent, from about 25 weight percent to about 75 weight percent, from about 30 weight percent The percentage is up to about 70 weight percent, from about 35 weight percent to about 65 weight percent, from about 40 weight percent to about 60 weight percent, or from about 45 weight percent to about 55 weight percent. Conversely, hard segments can exist in similar ranges. The 10 weight percent of the soft segment and the weight percent of the hard segment can be calculated based on data obtained from DSC or NMR. This method and the method of calculation are disclosed in U.S. Patent Application Serial No. 11/376,835, filed on March 15, 2006, by Colin, et al. No. 385,063-999, 558, entitled "Ethylene/A-Olefin Block Heterolog 15 Copolymer", which is hereby incorporated by reference in its entirety herein by reference in its entirety in its entirety in its entirety herein in If "crystallize, a singularity" is used, it has a first order transformation or crystalline melting point (Tm), which is measured by differential scanning calorimetry (DSC) or equivalent technique. This term can be used with "semi-crystalline". 'The word exchange is used. "Amorphous," the term refers to a polymer lacking a crystalline smear, as measured by differential scanning calorimetry (Dsc) or equivalent techniques. ''Multi-block copolymer' or 'segment copolymer, Equivalently means that a polymer comprises at least two chemically distinct regions or segments (referred to as "blocks"), preferably in a linear manner, that is, a polymer comprising chemically distinct units which are relatively symmetrical in 83 200911847 The alkylene functional group is bonded end-to-end, and is not pendant or grafted. In a preferred embodiment, the morphology and amount, density, and crystallization of the comonomer in which the block is incorporated The amount, the crystal size of the polymer of the composition, the isotactic pattern and degree (same row or row), the regional regularity or the 5 regional irregularity, and the branching amount including the long chain branch or the super branch Uniformity, or any other chemical or physical property. Multi-block copolymers are characterized by a unique distribution of both polydispersity index (PDI or Mw/Mn), block length distribution, and/or block number distribution, This is due to the unique process of making copolymers. More specifically When the polymer is produced in a continuous process, the polymer is expected to have a PDI of from 1.7 to 2.9, preferably from 1 to 8 to 2.5, more preferably from 1.8 to 2.2, and most preferably from 1.8 to 2.1. Manufactured in a batch or semi-batch process, the polymer has a PDI from h0 to 2.9, preferably from 1.3 to 2.5', more preferably from 1.4 to 2.0' and most preferably from 1.4 to 1.8. Ethylene/(X-olefin multi-block heteropolymer 15 (sometimes also referred to as "the heteropolymer of the invention" or "polymer of the invention") comprises ethylene and at least one copolymerizable a-olefin The comonomer is in a polymeric form, and the pot is characterized in that at least two of the multiblocks or segments of the polymeric unit having different chemical or physical properties (desired heteropolymer) are preferably a multi-block copolymer. The ethylene/(X-olefin heteropolymer) is characterized by at least one of the following two aspects. In one aspect, the ethylene/α-olefin poly-segment heteropolymer used in the embodiment of the present invention has about 1.7 to Mw/Mn ' of about 3.5 and at least one melting point of Celsius and density d' of g/cm3 Values correspond to the following relationship: 84 200 911 847

Tm > -2002.9 + 4538.5(d) - 2422.2(d) 2, and preferably H6288.1 + 13141(d) - 6720.3(d)2, and more preferably ^ 2858.91 - 1825.3(d) + 1112.8( d) 2. This k-point/density relationship is illustrated in Figure 1. Unlike the conventional ethylene/α-5 olefin random copolymer, the melting point of which decreases with decreasing density, the heterogeneous copolymer of the present invention (indicated by diamonds) exhibits a melting point substantially independent of density, especially when the density is between about 0_87 g/ Cc to about 0.95 g/cc. For example, when the polymer density is in the range of from 0.875 g/cc to about 0.945 g/cc, the polymer refining point is between about 110 ° C and about 130 ° C. In certain embodiments, when the density of the polymer is between 0.875 g/cc and about 0.945 g/cc, the melting point is in the range of from about ii5 °C to about 125 °C. In another aspect, the ethylene rhodium-olefin multi-block heteropolymer comprises ethylene and at least one alpha-olefin in a polymeric form and is characterized by a ΔΤ in degrees Celsius, which is defined as the highest differential scanning calorimeter ( The temperature of the peak of the DSC) is reduced by 15 to the temperature difference between the peaks of the highest crystallization analysis component (CRYSTAF), and the heat of fusion is ΔΗ of J/g, and ΔΤ and ΔΗ satisfy the following relationship: For ΔΗ up to 130 J/g, ΑΤ> -0·1299 (ΔΗ) + 62.81, and preferably AT 2-〇·ΐ299 (ΔΗ) + 64_38, and more preferably ΔΤ 2-〇.1299 (ΔΗ) + 65.95. Further, ΔΤ is greater than or equal to 13 〇 J/g, and ΔΤ is equal to or greater than 48 °C. The 20 CRYSTAF peak is a polymer accumulation assay using at least 5 percent (i.e., this peak must represent at least 5 percent of the cumulative polymer), and if less than 5 percent of the polymer has an identifiable CRYSTAF peak, the CRYSTAF temperature is 3 〇 ° C ' and Δ Η is the value of the heat of fusion at j / g. More preferably, the highest CRYSTAF peak contains at least 10% of the cumulative polymer. Figure 2 shows the data plot of the 85 200911847 dilute multi-stage polymer and the comparative examples. The integrated peak area and peak degree are calculated by a computer graphics program supplied by the equipment manufacturer. The diagonal line of the random ethylene octene comparative polymer is equivalent to the following equation ΔΤ = -0.1299 (ΔΗ) + 62.81. 5 In other aspects, the ethylene/α-olefin multi-block heteropolymer has a molecular component which is between 4 ° C and when the temperature is increased by the elution component (tref) 13〇. During the daytime elution, it is characterized in that the component has a higher comonomer content than the comparable random ethylene heteropolymer component eluted at the same temperature, preferably at least 5 percent higher than the mole copolymer. Preferably, the amount of body 3 is more than at least (7) percent, wherein the comparable random ethylene heteropolymer contains the same comonomer and has a melt index, enthalpy, degree, and molar comonomer content (based on all The polymer) is within 10 percent of the index, density, and molar comonomer content of the block heteropolymer (based on the total polymer). Preferably, the comparative heterogeneous copolymer 15 is also a percentage of Mw/Mn of the block heteropolymer and/or the comparable heteropolymer has a total comonomer content of Within 10% by weight of the content of the dissident heterogeneous copolymer. In still another aspect, the ethylene/α-olefin multi-block heteropolymer is characterized by a percent elastic recovery Re 2 测 measured at 300 percent strain and a helium cycle, in an ethylene/α_ The olefin heterogeneous copolymer is measured on a compressed film and has a enthalpy of one g/cc, degree d' and wherein when the ethylene/α-olefin heteropolymer has substantially no cross-linking phase, the values of Re and d satisfy the following relationship:

Re>1481-1629(d); and preferably Re>1491-1629(d); and more preferably 86 200911847 RQ 1501.1629(d); and most preferably ReM51M629(4). Fig. 3 shows the effect of the density of the unoriented film made of the specific copolymer of the present invention and the conventional random copolymer on the elastic recovery. For the same density, the heterogeneous copolymers of the present invention have substantially higher elastic recovery. 5 In certain embodiments, the ethylene/α·Chi multi-block heteropolymer - tensile strength above 10 MPa, preferably - tensile strength Μρ &, more preferably - resistance (four) degree MPa, And domain - at a crosshead (four) rate of at least 600 percent elongation at a rate of u cm / min, more preferably at least 7 〇〇 percent, more preferably at least 800 percent ' and most preferably at least 9 〇〇 One hundred and ten percentages. In other embodiments, the ethylene oxime-olefin multi-block heteropolymer has (1) a storage modulus ratio, G, (25t:) / G, (10 (rC), from 丨 to 刈, preferably From 1 to 20, more preferably from 1 to 10; and/or (2) less than 80% of 7 〇. 〇Compressive strain, preferably less than 70%, especially less than 6〇%, less than 15% 50%, or less than 40%, reduced to 0% compressive strain. In yet another embodiment, the ethylene/α-olefin multi-block heteropolymer is less than 80% of 7〇. (: compressive strain is less 7 at 7〇 (TC compressive strain ' is less than 60% of 7〇. (: compressive strain, or less than 5〇% of 7〇°c compression strain. Preferably, this heterogeneous copolymer is 7(rc The compressive strain is 20 to 40 percent less, less than 3 percent, less than 20 percent, and can be reduced to about 0 percent. In certain embodiments, the ethylene/α-olefin multi-block heteropolymer has a minor The thermal melting of 85 J/g, and/or the retardation strength of particles equal to or less than 100 psig (4800 Pa), preferably equal to or less than 5〇87 200 911847 lbs/ft2 (2400 Pa), especially equal to or less than 5 lbs/ft2 (240 Pa), and as low as 0 lbs/ft2 (0 Pa). In other embodiments, ethylene/cx-olefin heteropolymer The polymeric form comprises at least 50 mole percent of ethylene and has a compressive strain of 5 70 ° C of less than 80 percent, preferably less than 70 percent or less than 60 percent, most preferably less than 40 to 50 percent And in some embodiments, the multi-block copolymer has a PDI that conforms to the Schultz-Flory distribution, rather than a P〇isson distribution. The copolymer is further characterized by a polydispersity embedded The segment distribution and the multi-dispersion distribution of a block size have the largest possible distribution of block lengths. Preferably, the multi-block copolymer contains 4 or more blocks or segments, including terminal blocks. More preferably, the copolymer comprises at least 5, 1 Torr or 2 〇 blocks or segments, including terminal blocks. The comonomer content can be measured using any suitable technique, especially nuclear magnetic I5 resonance ("NMR"). Better spectrum. Furthermore, for polymers with relatively wide tref curves For polymers or blends, the polymer is expected to be first converted to a component, each having a elution temperature range of -1 (rc or less. That is, each elution component has -耽 or less The temperature window is collected. Using this technique, the block heterogeneous copolymer has at least one component having a higher molar component of the molar component than the comparable 20 different copolymers. The heterogeneous copolymer is a dilute smoke heteropolymer which preferably comprises ethylene and at least a copolymerizable comonomer in a polymerized form, characterized in that at least two of the polymerized monomer units having different chemical or physical properties are embedded. Segment or segment (residual polymer), most material-multiblock 200911847 copolymer. The block heteropolymer preferably has a peak (but not only a molecular component) eluting between 4 (TC and 130 ° C (but not recovering and/or separating the individual components), characterized in that the peak has A comonomer content, when calculated using the full width/half maximum (FWHM) area, is estimated by the infrared spectrometer 5 as having a random ethylene heteropolymer comparable to the same elution temperature and using the full The width/half maximum (FWHM) area is calculated as the peak of the amplification is a high average molar comonomer content, preferably above at least 5 percent, more preferably above at least 10 percent, and wherein the comparable random The ethylene heterogeneous copolymer comprises the same comonomer, and the melt index, density and molar 10 comonomer content (based on total polymer) are within 10 percent of the block heteropolymers. Preferably, this is comparable The Mw/Mn of the heterogeneous copolymer is also within 1% of the heterogeneous copolymer of the segment and/or the comparable heteropolymer has a total comonomer content of 10% by weight of the block heteropolymer. Inside. 15 full width The /half maximum (FWHM) area is calculated as the ratio of the thiol-independent fluorene-based response area in the ATREF infrared detector [CH3/Ch2], where the highest 绛 is identified by the baseline and then the FWHM area is determined. For the use of ATREF The distribution of the peak measurements, the FWHM area is defined as the area under the curve of 72, where several and D2 are the left and right sides of the ATREF peak, the peak height is divided into 20, and then the parallel baseline is drawn by a line. Left and right parts of the ATREF curve. A calibration curve for the comonomer content using a random ethylene/α-olefin copolymer is plotted against the FWHM area ratio of the NMR comonomer content relative to the TREF peak. This infrared method, calibration curve Produced using the same comonomer type as the tester. The 200911847 comonomer content of the olefin multi-block polymer iTREF peak can be determined by reference to the F WHM thiol·methylene area ratio of the TREF peak used [ The comonomer content can be determined using any suitable technique to optimize based on nuclear magnetic resonance (NMR) spectroscopy. Using this technique, the block heteropolymer has 5 alignments. Comparable heterogeneous copolymers have a high molar comonomer content. Preferably, a heteropolymer of ethylene and 1-octene, the block heteropolymer is eluted at 40 ° C to 130 ° C with TREF The comonomer content of the component is greater than or equal to the amount (-0.2013) T + 20.07, more preferably greater than or equal to the amount (-0.2013) T + 21.07, where T is a peak value of the peak elution temperature of a TREF component, in ° C indicates that Figure 4 illustrates an example of an acetamidine and a 1-octane block heteropolymer, which is a comonomer of several comparable ethylene/1-octene heteropolymers (random copolymers). The plot of the content relative to the TREF elution temperature, which corresponds to the line representing (-0.2013) T + 20.07 (solid line). The line of the equation (-〇·2〇13)Τ+21.07 is illustrated by the 15 dotted line. The comonomer content of the components of the several block ethylene/1-octene dissimilar copolymers (multiblock copolymers) of the present invention is also illustrated. All of the block heterogeneous copolymer components have significantly higher 丨-octene content than lines of equal elution temperature. This result is characteristic of the heterogeneous copolymers of the present invention, and is believed to be due to the presence of blocks having differences in the polymer chain, having both crystalline and amorphous properties. Figure 5 is a graph showing the polymer component of Example 5 (-multi-block copolymer) and Comparative Example F polymer (physical blend of two polymers using simultaneous polymerization of a two catalyst) TREF curve and comonomer content. For dipolymers from 40 to 13 (TC elution peak, preferably 60. (: to 95. (: the component is divided into two parts, each part is eluted at a temperature range of less than 10 ° C The actual data for the implementation of the 200911847 example is for example represented by a triangle. Those skilled in the art will be able to understand the calibration curve for the creation of heterogeneous copolymers containing different comonomers, and the comparison line used to match the TREF value has the same The monomer is a comparatively heterogeneous copolymer, preferably a random copolymer made of a gold olefin or other homogeneous catalyst composition. The heterogeneous copolymer of the present invention is characterized by a molar comonomer content greater than Preferably, the value determined by the calibration curve of the same TREF elution temperature is greater than at least 5 percent, more preferably greater than at least 1 percent. < _ In addition to the aspects and properties described herein above, the dilute hydrocarbon multi-drum segment The poly(1) conjugate is characterized by at least one additional feature. In one aspect, the olefin multi-block polymer is an olefin heteropolymer, preferably comprising ethylene in at least one copolymerizable form and at least one copolymerizable group. Comonomer A multi-block or segment (block heteropolymer) having at least two polymerized monomer units having different chemical or physical properties, preferably a multi-block copolymer having a heterogeneous total of 15 copolymers a molecular component eluted between 40 ° C and 130 ° C, which is characterized by having a TREF component when eluted between 40 ° C and 130 ° C. Preferably, the molar comonomer content of the comparable random ethylene heterogeneous component eluted at the same temperature is preferably at least 5 percent higher, more preferably at least 10, 15, 20 or 25 percent higher, wherein The comparable 20 random ethylene heteropolymers comprise the same comonomer, preferably the same comonomer, and the melt index, density and molar comonomer content (based on the total polymer) are ethylene/here. Within 10% of the α-smoke heteropolymer, the Mw/Mn of the comparable heteropolymer is also within 10% of the block dissimilar copolymer and/or the comparable heteropolymer Having a total of 91 200911847 comonomer content for the heteropolymer in the block Preferably, the heterogeneous copolymer is a heteropolymer of ethylene and at least one of a dilute hydrocarbon, especially a heteropolymer having an overall polymer density of from about 0.855 to about 0.935 g/cm3, and more In particular, and having a polymer having a comonomer greater than about 1 mole percent, the block heteropolymer has a comonomer content greater than or greater than the TREF component eluted between 4 Torr and 130 °C. Equal to the amount (-0·1356)Τ+13·89, preferably greater than or equal to the amount (-0·1356)Τ+14.93, and more preferably greater than or equal to the amount (-0·2013)Τ+21.07 ' Τ is the peak value of the TREF component of the comparison of the TREF component. C measurement. Preferably, 'for the aforementioned heteropolymer of ethylene and at least one alpha-anthracene', especially those having a total polymer density of from about 0.855 to about 0.935 g/cm3, and more particularly having greater than about The 1 molar percent comonomer polymer 'block heteropolymer has one at 4 Torr and 13 Torr. (^) The comonomer content of the TREF component of the large 15 or equal amount (_〇_2013) T+20_07, more preferably greater than or equal to the amount (-0·2013) Τ +21.07, where Τ is a comparison The peak elution temperature of the TREF component is determined by the same. In still another aspect, the hydrocarbon polyblock polymer is an olefin heteropolymer, preferably comprising ethylene and at least one in the polymerized form. Copolymerizable copolymerization

On monomer, characterized by at least two poly-segments or segments of a polymerized monomer unit having different chemical or physical properties (fragmented heterogeneous copolymer), preferably a multi-embedded copolymer, the block The heterogeneous copolymer is preferably a multi-block copolymer having a composition of TREF increments having a molecular weight of 40 ° (: and 130 °). Each component having a comonomer content of at least about 92,011,847,6 mole percent has a melting point greater than about 1 Torr (rc. For a component having a comonomer content of from about 3 mole percent to about 6 mole percent, Each component has a DSC melting point of about 1 〇〇c or higher. More preferably, the polymer component has at least 1 mole percent of comonomer, and 5 has a DSC melting point corresponding to:

Tm three (_5.5926) (molar percentage comonomer in the component) + 135.90 〇 In still another aspect, the olefin multi-block polymer is a monoolefin heteropolymer, preferably in a polymeric form A multi-block or segment (block heteropolymer) comprising ethylene and at least one copolymerizable copolymeric 10 monomer characterized by at least two polymerized monomer units having different chemical or physical properties, preferably a multi-embedded a segment copolymer having a molecular component eluted between 40 ° C and 130 ° C when using a TREF increment component, characterized in that each has an ATREF elution temperature greater than or A component equal to about 76 ° C has 15 as measured by DSC as melting entropy (hot melt) corresponding to the following formula: hot melt (J/gm) S (3.1718) (ATREF elution temperature (t:)) - 136.58 . The block heteropolymer of the present invention has a molecular component eluted between 40 ° C and 130 ° C when using the TREF increment component, characterized in that each has an ATREF elution temperature of 40X: at least At about 76. The component 20 has a melt entropy (hot melt) corresponding to the following formula as measured by DSC: hot melt (J/gm) S (1.1312) (ATREF elution temperature (°C)) + 22.97. The ATREF peak copolymerization of the infrared detector is known. The comonomer composition of the TREF peak of the product can be used as a 93 from the Polymer Char. of the city of Venecia, Spain (httg: //www.Polvmerchar.com/) 200911847 IR4 Infrared Detector Measurement. The “composition mode” of the detector is attached with a measuring sensor (CH2) and a composition sensor (CH3), which are fixed in the 2800-3000 cm-1 section. a narrow-band infrared filter. This measurement sensor detects methylene 5 (CH 2 ) carbon on the polymer (which directly relates to the polymer concentration in solution) while the composition sensor detects The sulfhydryl group (CH3) of the polymer is measured. The mathematical division of the composition signal (ch3) divided by the measurement signal (CH2) is sensitive to the total t-early content of the polymer measured in the solution and is responsive thereto. Corrected by the known standard for ethylene-smoke-smoke copolymer. 10 When using a detector with ATREF instrument, it can provide elution during the TREF method. Concentration of the compound (CH2) and composition (CH3) signal response. Specific correction of a polymer can be measured by measuring CH3 to CH2 with a known comonomer content polymer (preferably by NMR measurement). The area ratio is produced. The comonomer content of the ATREF peak of a polymer can be estimated by applying the respective CH3 and CH2 response ratios (i.e., the area ratio CH3/CH2 relative to the comonomer content). The area can be calculated using a full width/half maximum (FWHM) calculation after the appropriate baseline is applied to integrate the respective signals from the TREF map. The full width/half maximum (FWHM) area is calculated based on the ATREF infrared detector 20 The ratio of thiol to methylene response area [CH3/CH2], where the highest 绛 is discerned by the baseline and then determines the FWHM area. For the distribution measured using the ATREF peak, the FWHM area is defined as the under and the inter-curve The area 'where T' & T2 is the left and right sides of the ATREF peak divided into two, and then the parallel baseline draws a line across the left and right parts of the ATREF curve. 94 200911847 In this ATREF-infrared method Application infrared The spectrogram is based on the principle of measuring the comonomer content of a polymer similar to that described in the GPC/FTIR system as follows: Markovich, Ronald P.; Hazlitt, Lonnie G.; Smith, Linley; "Development of gel-permeation 5 chromatography-Fourier transform infrared spectroscopy for characterization of ethylene-based polyolefin copolymers” 0 Polymeric Material Science and Engineering (1991), 65, 98-100; and Deslauriers, PJ; Rohlfing, DC; Shieh, ET· ; “Quantifying short Chain branching Microstuctures in 10 ethylene-1-olefin copolymer using size exclusion chromatography and Fourier transform infrared spectroscopy (8£(3-?丁111)',,? 〇 1 > 〇 1161' (2002), 43, pp. 59-170, the entire contents of which are incorporated herein by reference. In other embodiments, the multi-block ethylene/α-olefin heteropolymer is characterized by an average block index ΑΒΙ greater than 0, and up to about 1.0, and a molecular weight distribution Mw/Mn greater than about 1-3. The average block index ΑΒΙ is the weight average of the block index ("BI") of each polymer component obtained by preparing TREF in increments of 5 ° C from 20 ° C to 110 ° C: 20 where Bli is the invention The ethylene/(X-olefin heteropolymer) block index of the ith component obtained in the prepared TREF, and Wi is the weight percentage of the ith component. For each polymer component, BI is defined by the following two equations (both The same BI value can be obtained):

:1 / 匕_ 1 / milk 4 βτ _ LnPx - LnPx0 ~l/TA-\/TAB ^ J~~LnPA-LnPA 95 200911847 where Τχ is the pre-ATREF elution temperature for the i-th component (preferably Keivin No), Ρχ is the ethylene molar component of the i-th component, which can be measured by NMR or IR as described above. PAB is the ethylene molar component of the all ethylene/α-olefin heteropolymer (before componentization), which can also be measured by NMR or IR. ΤΑ&ΡΑ is the pure "hard chain 5 segment" (which refers to the crystalline segment of the heteropolymer) and the ATREF elution temperature and the ethylene molar component. As the approximation of the first stage, if the "hard segment, the actual value is not available" then the ΤΑ & ΡΑ value is set for the high density polyethylene homopolymer. For the calculations performed herein, ΤΑ is 372 ° Κ, ΡΑ is 1. TAB is the ATREF temperature of the same composition and the unreacted copolymer having a ρ ΑΒ ethylene molar component. ΤΑΒ can be calculated by the following equation:

Ln Ραβ = α / ΤΑΒ + β, where (X and β are two constants, which can be determined by using a known random ethylene copolymer correction. Note that α and β may vary from instrument to instrument. It is necessary to generate its own calibration curve based on the detected polymer composition, and also to use a similar molecular weight range such as a component. This has a small molecular weight effect. If the calibration curve is obtained from a range of similar molecular weights, this effect is substantially It is negligible. In certain embodiments, the random ethylene copolymer satisfies the following relationship:

Ln P = -237.83/Tatref + 〇_639. TXO is the ATREF temperature of a random copolymer having the same composition and having a oxime component ρχ. Τχο can be calculated from LnPx = α/ΤΧ0 + β. Conversely, Ρχο is an ethylene molar component having the same composition and having an ATREF temperature Τχ random copolymer, which can be calculated from 1^1?乂〇=〇1/丁?(+0. Once each prepared TREF is obtained The block index (ΒΙ) of the component can be calculated as the weight average block index ABI of the total polymer of 96 200911847. In certain embodiments, the ABI is greater than 〇' but less than about 〇3, or from about 0.1 to about 〇 3. In other embodiments, 'ABI is greater than about 〇3' and is about 1 〇. Preferably, abi is between about 0.4 and about 〇7, between about 〇5 and about 〇. • between 7 ranges, or between about 6 5 and about 0.9. In certain embodiments, the ABI ranges from about 〇3 to about 〇.9, between about 0.3 and about 0.8, or about Between 0.3 and about 0.7, between about ο" to about 0.6, between about 〇3 to about 〇.5, or between about 〇3 and about 。4. In other embodiments, the ABI is about 0.4 to Between the range of about ο5, about 5 to about 1_〇, or between about 0.6 and about 1. ,, about 7 to about 1 10 10, about 〇·8 to about 1.0, or about 〇.9 to about 1 ·〇 range Another characteristic of the multi-stage ethylene/α-olefin heteropolymer is that the multi-block ethylene oxime-olefin heteropolymer comprises at least one polymer component which can be prepared by borrowing a TREp^^, wherein the component has a block index greater than Approximately 1 and up to about i_〇, and a molecular weight fraction mMw/Mn is greater than about 丨 3. In some embodiments, the polymer component has a block index greater than about 0.6 and up to about 1.0, Greater than about 〇7 and up to about ι·〇, greater than about 〇8 and up to about 丨〇, or greater than about 0.9 and up to about 1. 〇. In other embodiments, the polymer component has embedded The number of turns is greater than about 〇.1 and up to about 丨〇, greater than about 〇2 up to about 丨〇, greater than about 0.3 up to about ι_〇, greater than about 〇4 and up to about 丨〇, or greater than about 20 〇 And in other embodiments 117, the polymer component has an inset k number greater than about 〇1 and up to about 0.25, greater than about 〇2 and up to about 〇·5, Greater than about 0.3 and up to about 〇5, or greater than about 〇4 and up to about 〇 5. In still other embodiments, the polymer component has a block index greater than about 〇2. And up to about 0.9, greater than about 〇3 and up to about 〇8, greater than about 〇4 and up to about ,7, or 97 200911847 greater than about 0.5 and up to about 0.6. For copolymerization of ethylene and a-olefins Preferably, the multi-block heteropolymer has (1) a PDI of at least 1.3', more preferably at least 1.5', at least 1 Å, or at least 2 Å, and most preferably at least 2.6, up to a maximum of 5.0. More preferably, the highest value is as high as 3.5 and the highest value is 2.7; (2) - hot melting is 80 J/g or less '(3) - ethylene contains Dong At least 50 weight percent; (4) a glass transition temperature Tg of less than -25C, more preferably less than -30 °C, and / or (5) - and only one Tm. Further, the multi-block heteropolymer may have a storage modulus G alone or in combination with any of the other properties disclosed herein such that log(G,) is at a temperature of 1 Torr. (: greater than or equal to 400 kPa' is preferably greater than or equal to 丨〇Mpa. Further, the multi-block heteropolymer has a relatively flat storage modulus at a temperature between 〇 and l〇〇 °C ( This is illustrated in Figure 6), which is a property of block copolymers, but previously unknown olefin copolymers also have this property, especially copolymers of ethylene 15 and at least one C3-8 aliphatic alpha-lean. (In this context, the term "relatively flattery" means log G, (as Pa) decreasing between 50 and 100 t in less than -, preferably between 0 and 100 ° C.) The heterogeneous copolymer is further characterized by a penetration depth of at least 9 (rc mechanical analysis of 1 mm' and a flexural modulus of 3 kpsi (2 〇 20 MPa) to 13 kpsi (90 MPa). The segmented heterogeneous copolymer may have a thermomechanical analysis penetration depth of 1 mm at a temperature of at least 104 C and a flexural modulus of at least 3 kpsi (20 MPa) characterized by wear resistance (or volume loss). Less than 90 mm3. Figure 7 shows the relative flexibility of TMA (1 mm) compared to other known polymers. 98 200911847 This multi-part copolymer has a significantly better balance of heat and heat resistance than other polymers. In addition, the multi-block ethylene/α-olefin heteropolymer has a 〇〇1 to 2_g/ΙΟ minute. (4) Index 12, preferably a melt index 5 index l2 of reading to the surface _ minute, more preferably a melt index 12 of 0·01 to 5 (nine) g/ιο minutes, and especially a melting of 〇_〇1 to 100 g/io minutes. Index 2. In a specific embodiment, the ethylene/α-dilute polymer has a melting index of (4) money g/1 G minutes, a melting index of 〇5 to 50 g/l 〇 minute, 丨 to 卯 _ minute The smelting index I" 1 to 6 g / l 〇 minutes of the melt index 丨 2 or 〇 3 to 1 〇 g / 1 之 melting 1 〇 index 12. Pure implementation of the wealth, this eththene / α _ smoke The polymer has a swell index of lg/ΙΟ minutes, 3 g/ΙΟ minutes or 5 g/ιο minutes. Multi-block heteropolymers can have from 〗 〖000 g/m to 5, 〇〇〇, 〇〇〇 The molecular weight Mw of g/mole is preferably 1 〇〇〇g/mole to 丨, 〇〇〇, 〇〇〇g/mole molecular weight, more preferably 10,000 g/mole to 5 〇〇, 〇 〇〇g/mole molecule 15 The amount, especially from 10,00 〇g/mole to 300,000 g/mole. The density of the olefin multi-block polymer is from 0.80 to 0.99 g/cm3. The density of the ethylene-containing polymer is preferably from 0 to 85 g/cm3. To 0.97 g/cm 3. In a particular embodiment, the ethylene/α-olefin polymer has a density ranging from 0.860 to 0.925 g/cm 3 or from 0.867 to 0.910 g/cm 3 . 20 A method of making a multi-block heterogeneous copolymer has been disclosed in the following patent application: U.S. Patent Application Serial No. 60/553,906, filed on March 17, 2004; Patent Provisional Application No. 60/662,937; U.S. Patent Provisional Application No. 60/662,939, filed on March 17, 2005, filed on March 17, 2005; PCT Patent Application No. PCT/US2005/008916, filed March 17, 2005; PCT Patent Application PCT/US2005/008915 filed on March 17, 2005; and The PCT 5 patent application PCT/US2005/008917 filed on Jan. 17, the entire disclosure of which is hereby incorporated by reference. For example, one such method comprises contacting ethylene and optionally with at least one non-ethylene polymerizable monomer with a catalyst composition under conditions of addition polymerization, comprising: a blend formed by combining the following Or reaction product: 10 (A) - a first olefin polymerization catalyst having a high comonomer incorporation index, (B) - a comonomer incorporation having a comonomer incorporation index less than the catalyst (A) 90% of the index of the second olefin polymerization catalyst, preferably less than 50% 'more preferably less than 5 percent, and 15 (C) one chain shuttling agent. Representative catalysts and chain shuttling agents are as follows. The catalyst (A1) is [N-(2,6-bis(1-methylethyl)phenyl)decylamino)(2-isopropylphenyl)(α-naphthylene-2-yl (6) -pyridin-2-yl)methane)] decyl dimethyl, which is based on the patent application of WO 03/40195, 20 2003 US 0 020 017, US SN 10/429, 024, and WO 04/24740, filed on May 2, 2003. Teaching preparation. 100 200911847 ch(ch3)2

(H3C)2HC ch3 Catalyst (A2) is [N-(2,6-bis(1-methylethyl)phenyl)decylamino)(2-methylphenyl)(1,2-phenylene) --(6-πΛσ定亚-2-yl)methanthine)] dimethyl to 'WO 03/40195, 2003 US0204017, USSN 10/429,024 and WO 04/24740, filed on May 2, 2003 The teaching of the patent application is prepared.

The i catalyst (A3) is bis[1^3'''-(2,4,6-tris(methylphenyl)nonylamino)ethylenediamine]diphenylmethyldibenzofluorene.

Catalyst (A4) is bis 2-oxoyl-3-(dibenzo-1H-indol-1-yl)-5-(methyl)phenyl)-2-phenoxymethyl)cyclohexane -1,2-Diyldibenzo-zirconium (IV), 101 200911847 Substantially prepared according to the teachings of US-A-2004/0010103.

The catalyst (B1) is 1,2-bis-(3,5-di-t-butylphenylene)(1-(N-(1-decylethyl)immino)methyl)(2-oxygen) Mercapto) dibenzopyrene. c(ch3)3

The catalyst (B2) is 1,2-bis-(3,5-di-t-butylphenylene) (1-(Ν-(2-fluorenylcyclohexyl)-immino)indolyl) (2- Oxyfluorenyl) dibenzo-fault. (h3c)3

The catalyst (Cl) is (t-butylammonium) dimethyl (3-N-.pyrrol 10 -1,2,3,33,7&-11-indol-1-yl)decane dioxime Base titanium, the essence of which is prepared according to the teachings of 1^? 6,268,444: 102 200911847

Catalyst (C2) is (t-butylammonium) bis(4-mercaptophenyl)(2-methyl-l,2,3,3a,7a-r|-indol-1-yl) The dimethyl dimethyl sulphate is prepared according to the teachings of US-A-2003/004286:

The catalyst (C3) is (t-butylammonium) bis(4-mercaptophenyl)(2-methyl-l,2,3,3a,8a-r)-s-indacen-l-yl ) Shi Xi Shao Dimethyl Titanium, the essence of which is prepared according to the teaching of US-A-2003/004286:

10 Catalyst (D1) is bis-mercaptodioxane (s--1-yl) ruthenium dichloride available from Sigma-Aldrich: 103 200911847

The shuttle agent allows the hand shuttle to include diethyl zinc, di(i-butyl)zinc, di(n_美美), triethylaluminum, trioctylaluminum, ethylgallium, i-butylaluminum. Dimethyl (t-butyl) 5 oxane), i-butyl aluminum bis(trimethylsulfonyl) decylamine, n-octyl bis(. , bis(η-octadecyl)i-butylaluminum, butyl-di-bis-amp;pentyl)amide, η-octylbis 2,6-di-t-butylphenoxylated aluminum, η_辛基铭Bis(ethyl(1-naphthyl)decylamine), ethylbis(t-butyldidecylphosphonium)aluminum, ethylamine (indenyl fluorenyl) guanamine, ethylaluminum double 2 , 3,6,7-dibenzo-1_azepine to give 10 decylamine), n-octyl aluminum bis 2,3,6,7-dibenzo-1_azepane decylamine n) Octyl bis (t-butyl) decyl aluminum, ethyl (2,6-diphenylphenoxy), and ethyl (t-butoxy). Preferably, the foregoing process employs a continuous phase solution process to form a block copolymer, especially a multi-block copolymer, preferably a at least two monomeric linear poly-segment copolymer, more particularly ethylene and C3-2 is a thin or ring-dilute smoke, and more preferably ethylene and a C4.2Q alpha-olefin, which uses a multi-catalyst that cannot be internally converted. That is, the catalyst is chemically different. This process is ideally suited for the polymerization of monomer mixtures in high monomer conversion under continuous solution polymerization conditions. Under these polymerization conditions, the shuttle of the chain shuttling agent to the catalyst is advantageous in the growth of the chain compared to 104 200911847, and the multi-block copolymer, particularly the linear multi-block copolymer, is formed with high efficiency. Multi-block heteropolymers differ from conventional random copolymers, physical blends of polymers, and block copolymers prepared via continuous monomer addition, conversion catalyst, anionic or 5 cationic living polymerization techniques. In particular, the heterogeneous copolymers of the present invention have better (higher) heat resistance, higher TMA penetration as measured by melting point, as compared to random copolymers of the same monomer and monomer content of equal crystallinity or modulus. Temperature, high temperature tensile strength, and / or higher temperature torque storage modulus measured by dynamic mechanical analysis. Compared with the random copolymer containing the same monomer and monomer content, the heterogeneous copolymer of the present invention has a lower compressive strain, especially when the temperature is increased, and has lower stress relaxation, higher anti-potential denaturation, and higher Tear strength, high anti-caking property, faster preparation due to higher crystallinity (curing) temperature, higher recovery (especially when warming), better wear resistance, higher shrinkage force and Preferred oil and filler acceptability. 15 This multi-block heteropolymer also exhibits unique crystallization and branching relationships. That is, the heterogeneous copolymer of the present invention has a relatively large difference between the highest peaks when measuring the hot melt function using CRYSTAF and DSC, especially random copolymerization containing the same monomer and monomer amount at equal total density. A physical blend of the material or polymer, such as a blend of high density polymer and lower density co-polymer. It is believed that the unique characteristics of the heteropolymers of the present invention are due to the unique distribution of comonomers within the blocks in the polymer chain. In particular, the heterogeneous copolymers of the present invention may comprise alternating blocks of different comonomer contents, including homopolymer blocks. The heteropolymer of the present invention may also comprise a number of polymer blocks of different densities or comonomer contents and/or a block size of 105 200911847, which is a Schultz-Flory type distribution. In addition, the heterogeneous copolymers of the present invention also have a unique peak melting point and crystallization temperature profile which is substantially independent of polymer density, modulus and type. In a preferred embodiment, the microcrystalline order of the polymer indicates the characteristics of the crystal spheres and layers that differ from the random or block copolymer, 5 even at a PDI value of less than 1.7, or even less than 1.5, at least 1.3. Further, the multi-block heteropolymer can be prepared using techniques that affect the extent or amount of the block. That is, the amount and length of comonomer of each polymer block or segment can be varied by controlling the ratio and form of the catalyst and shuttling agent, as well as the temperature of the polymerization and other polymerization variables. The surprising 10 advantage of this phenomenon is the discovery of an increase in the degree of blockage, improving the optical properties, tear strength, and high temperature recovery properties of the resulting polymer. In particular, as the average number of blocks in the polymer increases, the clarity, tear strength, and high temperature recovery properties increase and the atomization decreases. By selecting a shuttle and a combination of catalysts with the desired chain transfer capability (high rate shuttle with low chain termination), other forms of polymer termination are effectively suppressed. Thus, in the examples of the present invention, if there is a small amount of β-hydride in the polymerization of the ethylene/α-olefin comonomer mixture, and the resulting crystalline block is highly or substantially completely linear, With little or no long chain branching. Polymers having highly crystalline chain ends can be prepared selectively 20 according to embodiments of the invention. In elastomer applications, reducing the relative amount of the polymer terminated by the amorphous block reduces the intramolecular dilution effect on the crystalline region. This result can be obtained by selecting a chain shuttling agent and a catalyst having an appropriate response to hydrogen or other chain terminators. In particular, the catalyst that produces a highly crystalline polymer is more resistant than the catalyst that produces less crystalline polymer segments (eg, the incorporation of higher copolymers 106 200911847 bodies, or the formation of disordered polymers) Easily chain termination (e.g., by the use of hydrogen), the highly crystalline polymer segment will preferentially occupy the terminal portion of the polymer. Not only the end groups are formed, but when terminated, the highly crystalline polymer formation sites are again used for the re-starting of polymer formation. This initially formed polymer is thus another highly crystalline polymer segment. Therefore, the two ends of the resulting multi-block copolymer are preferably highly crystalline. The heterocopolymer for use in the practice of the present invention is preferably a heteropolymer of ethylene and at least one C3-C20 alpha-olefin. A copolymer of ethylene and a C3-C20 α-ene Fe is preferred. The heteropolymer may further comprise 10 C4-C18 diolefin and/or alkylbenzene. Suitable unsaturated comonomers which can be used for the polymerization with ethylene include, for example, ethylenically unsaturated monomers, conjugated or non-conjugated dienes, polyolefins, C3-C20 alpha-olefins such as alkylbenzenes and the like. Examples of such comonomers include, for example, propylene, isobutylene, butene, κ hexene, decene, 4-methyl-1-pentene, 1-heptene, 1-octene, 1-decene , κ decene and its likes. 15 1-butene and 1·octane reduction. Other suitable monomers include styrene, halo- or alkyl-substituted styrene, vinylbenzocyclobutane, hexamethylene dichloride, 1,7-octadiene and cycloalkanes (eg cyclopentane) Alkene, cyclohexene and cyclooctene). While ethylene/α-dilute hydrocarbon multi-block heteropolymers are preferred polymers, other acetam/olefin polymers can also be used. The olefin used in the present invention means a group of 20 unsaturated tobacco compounds having at least a carbon-carbon double bond. Optional Catalysts Any of the dilute hydrocarbons may be used in embodiments of the invention. Preferably, the suitable olefin is a C3_C2 steroidal and aromatic compound containing an ethylenic unsaturated, and a compound such as cyclobutene, cyclopentadiene, dicyclopentadiene and norbornne, Restricted to be substituted with a cl_C2 hydrazine or a cyclic hydrocarbon group at positions 5 and 6 of 200911847 norbornene. And a mixture of the olefins and a mixture of the olefins and the C4-C40 diolefin compound. Examples of olefin monomers include, but are not limited to, propylene, isobutylene, 1-butene, 1-pentene, 1-hexene, 1-heptene, 1-octene, 1-decene, 1-decene, and 1-twelve, 1-fourteen, 1-hexadecene, 1-octadecene, 1-tap, 3-mercapto-1-butene, 3-methyl-1-pentene, 4-methyl-1-pentene, 4,6-dimethyl-1-heptene, 4-vinylcyclohexene, vinylcyclohexane, norbornadiene, ethylidene norbornene, cyclopenta Alkene, cyclohexene, dicyclopentadiene, cyclooctene, C4-C40 dienes, including but not limited to 1,3-butadiene, 1,3-pentadiene, 10 1,4-pentane Alkene, 1,5-pentadiene, 1,7-octadiene, 1,9-decadiene, other C4-C40 α-dilute hydrocarbons, and the like. In a particular embodiment, the alpha-lean hydrocarbon is propylene, 1-butene, 1-pentene, 1-hexene, 1-octene, or combinations thereof. Although any vinyl-containing hydrocarbon can be used in the examples of the present invention, when the molecular weight of the monomer becomes too high, practical problems such as monomer availability, cost, and 15 can be conveniently removed from the ungenerated polymer. The ability to react unreacted monomers becomes a greater problem. The polymerization described in the present invention is very suitable for the production of an olefin polymer containing a monoethylidene aromatic monomer, the monomer styrene, fluorenyl-mercaptostyrene, fluorene-methylstyrene, t-butylbenzene Ethylene and its similarities. In particular, heteropolymers comprising ethylene oxide and styrene can be prepared by the teachings herein below. Alternatively, a copolymer of ethylene, styrene and a C3-C20 alpha-olefin having improved properties may be prepared which optionally contains a C4-C20 diene copolymer. Suitable non-conjugated diene monomers can be a linear, branched or cyclic hydrocarbon diene having from 6 to 15 carbon atoms. Illustrative of suitable non-conjugated dienes include, but not limited to, 108 200911847 . 5 not limited to linear acyclic dienes such as 1,4·pentadiene, 1,6-octadiene, 1,7-octadiene, 1,9-decadiene, branched acyclic adiene such as 5-methyl-1,.4-hexadiene; 3,7-dimethyl-1,6-octadiene; 3,7-di a mixed isomer of methyl-1,7-octadiene and dithiydromyricene and dihydroocinene, a monocyclic alicyclic diene such as 1,3_cyclopentadiene; Iso,4_cyclopentadiene; 1,5-cyclooctadiene and iota,5-cyclododecadiene, and polycyclic alicyclic fusion and bridge e'-ene-ene such as tetrahydroanthracene, methyl Tetrahydroindole, dicyclopentadiene, bicyclo-(Hu.septa-2,5-diene; alkenyl, alkylene, cycloalkenyl and cycloalkylene norbornene such as 5-methylene-2 _norbornene (MNB); 5_propylene_2_norbornene, 5 iso 10 propylene-2-norborn, 5_(4·cyclopentene)_2_norborn, 5_cyclohexylene 15 £ K > ·2·Ice borneol, 5-vinyl-2-norbornene and norbornadiene. Basically, the diene of EPDM is especially diene!, 'hexadiene (HD), 5_亚亚^Ice icing thin (ENB) 5_ alkylene group _2_ ethylene-norbornene (VNB), 5- ^ precipitation particular sheet gradually MNB), and dicyclopentadiene dilute (DCPD) is preferred. The olefin (HD乂) is preferably a rare metal of 5·ethylene '2 — norbornene _NB) and K hexan 20 ethylene I — a known example of the present invention - the expected polymer of the group is 0f heterogeneous k(10) palpitations and optional elastomers of at least two dilute monomers. 6 cc C3_C2 〇a_ smear is especially propylene. For use in the present invention, wherein R*, the preferred a-lean smoke is a linear m county having a chemical SCH2 = CHR*, a Γ having a liver of 1 to 12 carbon. Suitable for suigui, i include but not limited to propylene, isobutylene, 1-butadiene, 1- for cyanide. _ 4_methyl pentane and 1_xin return. A particularly good a-dilute hydrocarbon. This propylene polymer is generally referred to in the art as a 卩 or 109 200911847 EPDM polymer. Dilutions suitable for the preparation of such polymers, particularly multi-block E P D Μ type polymers include co-light or non-common, linear or branched-chain or polycyclic dienes of 4 to 2 〇 carbon. Preferred dienes include hydrazine, 4-pentadiene, 1,4-hexadiene, 5-ethylidene-2-norbornene, dicyclopentadiene, cyclohexadiene, 5 5-butylene 2 for borneol. - A particularly preferred dilute is iminoethyl-2_norbornene. Since the diene-containing polymer comprises alternating segments or blocks having a greater or lesser amount of dienes (including none) and alpha-olefins (including none), the total of the dienes and the oxime may be The loss is reduced by subsequent polymer properties. That is, since 10 is a diene and an α-olefin monomer, it is preferentially incorporated into a type of polymer block, rather than uniformly or randomly incorporated into a polymer, which can be effectively utilized and can be preferably controlled subsequently. The crosslink density of the polymer. The crosslinkable elastomer and the cured product have advantageous properties including higher tensile strength and better elastic recovery. 15 In certain embodiments, a heterogeneous copolymer of the invention prepared by a two-catalyst having varying amounts of comonomer having a block weight ratio of 95:5 to 5:95 thus formed. The elastomeric polymer is expected to have an ethylene content of from 20 to 90%, a diene content of from 01 to 10%, and a decene content of from 10 to 80% in the total weight of the polymer. More preferably, the multi-block 20 elastomeric polymer has an ethylene content of from 60 to 90% by weight based on the total weight of the polymer, a diene content of from 0.1 to 10%, and a hydrocarbon content of from 1 to 4%. content. Preferred polymers are high molecular weight polymers having a weight average molecular weight (Mw) of from -1 Torr to about 2,500,000, preferably from 2 Torr, from 〇〇〇 to 500,000, more preferably from 20,000 to 350, 〇 〇〇, and polydispersity is less than 3 $ 110 200911847 more preferably less than 3.0, and a 1 to 25 摩 Mouni viscosity (ML (1+4) 125 C) ° better, this polymer has 65 to 75 percent ethylene content, 〇 to 6 percent diene content 'and 2 〇 to 35 percent... dilute hydrocarbon content. Catalyst 5 If the term “overnight” is used to refer to a time of approximately 16-18 hours, the term “room temperature” means 20-25. (: The temperature of the mixture, and the term "mixed alkane," which refers to the commercially available C6 September sulphur mixture" can be obtained by Exx〇nM〇bii Chemical under the trademark isopar E®. The name of the compound in this document In the case where the structure is inconsistent, the structure indicator is to be inspected. The synthesis of all metal mismatches and the preparation of all screening experiments are carried out in a dry nitrogen atmosphere using a dry box technique. HpLC grade, and dried in its use. MMAO refers to a modified methyl aluminoxine, a tri-aluminum-modified methyl aluminoxane commercially available from Akzo-Noble. The preparation of B1) is carried out as follows: 15)) (2-hydroxy-3.5-di-di-butyrate) Mo Mo) Preparation of a convex face 3,5-di-t-butyl salicylaldehyde (3〇〇g) This was added to 1 mL of isopropylamine. The solution was quickly evaporated to light yellow. After stirring at room temperature for 3 hours, the volatiles were removed in vacuo to yield a pale yellow, crystalline solid (97% yield). 20 (b)-L2-bis-(3,5-di-t-di-yl-lamyl-a-methyl)ipimino)!)) (2-oxo) a dioxin* surname, -(1- A solution of 2-ethyl-3,5-di(t-butyl)phenylimine (6〇5 mg, 2.2 mmol) in 5 mL of toluene was slowly added to Zr(CH2ph)4 (500 mg, U mm〇i) in a solution of 50 mL of toluene. The resulting black yellow 111 200911847 solution was thrown off for 30 minutes. The solvent was removed under reduced τ „ 八 戍 pressure to produce a reddish brown solid. Expected product. The preparation of the catalyst (B2) was carried out as follows. (2 gas sulfhydryl-3,5-di(t-butyl) moslar 5 yl) imine preparation 2 methylcyclohexylamine (8·44 眺, 64 〇 paw 〇 1) dissolved in methanol (9 〇 Add a-t-butyl salicylate (1〇〇〇g, 42 67 face 〇ι) to the claw [). The reaction mixture was stirred for 3 hours and then cooled to a pit for 12 hours. The resulting yellow solid sink was collected and treated with cold methanol (2 χ 15 rinsing and then dried under reduced pressure. Yield: "17 g of yellow solid. lH] SfMR is consistent with the expected product, which is a different a mixture of structures. (b) Double ^ B) (2-1 醯-3,5-two (t-丁) phenyl)immino) 二茉#chain less ^ % one (1-(2- A solution of decylcyclohexyl)ethyl)(2_oxoyl-3,5-di(t-butyl)benzene 15-yl)imide (7.63 g '23.2 mmol) in 200 mL of hydrazine was slowly added to Zr ( CH2Ph)4 (5.28g, n.6mm〇i) in a solution of eoomL toluene. The resulting black-yellow solution was at 25. (: stirring for 1 hour. This solution was diluted with 680 mL of toluene to obtain a solution having a concentration of 0.00783 Μ. Co-catalyst 1 20 a mixture of tetrakis(pentafluorophenyl)borate methyl di(C14_18 alkyl)ammonium salt (hereinafter referred to as arrneenium borate), which is composed of long chain trialkylamine (ArmeenTM) M2HT, available from Akzo-Nobel, Inc., HC1 and Li[B(C6F5)4], is essentially as disclosed in Example 2 of usp 5,919,983. 112 200911847 Cocatalyst 2 Mixed Bis(pentafluorophenyl) )-alane)-2-11 Ci4i8 alkyl decyl ammonium salt of imidazolidine, prepared according to Example 16 of USP 6,395,671. Shuttle Agent 5 The shuttle used includes diethyl (DEZ, 25 SA1), bis(丨-butyl) zinc ( SA2), bis(n-hexyl)zinc (SA3), triethylaluminum (TEA, SA4), trioctylaluminum (SA5), triethylgallium (SA6), 丨-butylaluminum bis ( T_butyl) siloxane (SA7), i-butyl aluminum bis(trimethyl decyl) decylamine (SA8), & octyl bis (pyridyl methoxy) aluminum (SA9 ), bis(η-octadecyl)_i_butylaluminum 10 (SA10), "butylaluminum bis(η-pentyl)decylamine) (SA11) 'η-octyl bis 2,6_ di- T-butylphenoxy)aluminum (SA12), ~octylaluminum bis(ethylnaphthyl)amine XSA13), ethylbis-t-butyl(dimethylmethoxy)aluminum (SA14), B Aluminium (bistrimethylhydrazinyl) decylamine (SA15), ethylaluminum bis 2,3,6,7-dibenzo-i-azepane decylamine (SA16), η-xin Base aluminum bis 2,3,6,7-dibenzo-1-azacycloheyl 15 heptane decylamine) (SA17), η-octyl bisdimethyl (t-butyl) oxime (SA18) ), ethyl (2,6-diphenyloxy)zinc (SA19), and ethyl (t-butoxy) (SA20). Example 1-4, Comparative Example AC General High Yield Parallel Polymerization Conditions 20 Polymerization was carried out using a high throughput, parallel polymerization reactor (PPR) from Symyx Technologies, Inc., and substantially in accordance with U.S. Patent Nos. 6,248,540, 6, 03,917, The disclosure of 6,362,309, 6,306,658 and 6,316,663. Ethylene copolymerization was carried out at 130 ° C and 200 psi (1.4 MPa), depending on the desired ethylene, based on the total catalyst used, 1.2 equivalents of co-catalyst 1 113 200911847 (in the presence of MMAO, 丨丨 equivalent). A series of polymerizations were carried out in a bridging pressure reactor (PPR) containing 48 pre-weighed glass tube independent reactor units in a 6 χ 8 array. The operating volume in each reactor unit is 6000 μί. Control the temperature and pressure of each unit and stir with the respective paddles. This monomer gas and quench gas are fed directly into the PPR unit by a tube and are controlled by an automatic valve. The liquid reactant is automatically added to each reactor unit by means of an injector, and the reservoir solvent is a mixed alkane. The order of addition is a mixed alkane solvent (4 ml), ethylene, 1-octene comonomer (1 ml), cocatalyst 1 or a common catalyst 1/MMAO mixture, a shuttling agent, and a catalyst or catalyst 10 mixture. When a mixture of co-catalyst 1 and MMAO or a mixture of two catalysts is used, the reagent is premixed in a vial immediately prior to addition to the reactor. When a reagent was omitted in an experiment, the aforementioned order of addition was maintained. The polymerization is carried out for about 1-2 minutes until a predetermined ethylene consumption is reached. After quenching with CO, the reactor was cooled and the glass tube was removed. The tube was moved to a 15 core/vacuum drying unit and dried at 6 ° C for 12 hours. The tube containing the dried polymer was weighed and the difference between this weight and the weight of the tare was the net yield of the polymer. The results are shown in Table 1. In Table 1 and elsewhere in the description of the invention, comparative example compounds are indicated by an asterisk (*). Examples 1-4 illustrate the 20 synthesis of the linear block copolymer (multiblock) of the present invention, as presented by the formation of a very narrow MWD, substantially as a monotype copolymer when DEZ is present, and in the absence of DEZ In the presence of a double-type, broad molecular weight distribution product (a separately produced polymer mixture). Due to the fact that the known catalyst (A1) can incorporate more octene than the catalyst (B1), the different blocks or segments of the resulting copolymer of the present invention are separable in branching or density. 114 200911847 Table 1 Ex. Cat. (Al) Cat. (Bl) (μιποί) (μηιοί) Cocat (μιηοΐ) MMAO (μηιοί) Shuttle (μηιοί) Yield (g) Mn Mw/Mn Hexyl 1 A* 0.06 - 0.066 0.3 - 0.1363 300502 3.32 - B* - 0.1 0.110 0.5 - 0.1581 36957 1.22 2.5 C* 0.06 0.1 0.176 0.8 - 0.2038 45526 5.302 5.5 1 0.06 0.1 0.192 - DEZ (8.0) 0.1974 28715 1.19 4.8 2 0.06 0.1 0.192 - DEZ (80.0) 0.1468 2161 1.12 14.4 3 0.06 0.1 0.192 - TEA (8.0) 0.208 22675 1.71 4.6 4 0.06 0.1 0.192 - TEA (80.0) 0.1879 3338 1.54 9.4 1 C6 or higher chain content per 1000 carbon 2 Dimorphic molecular weight distribution 5 Visible The multi-block polymer produced by the present invention has a narrow polydispersity (Mw/Mn) and a larger block-copolymer content than the polymer produced in the absence of a shuttling agent (trimer, tetra Polymer, or larger). Further characteristic data for the polymers of Table 1 can be determined in conjunction with Figures 1-7 and the drawings in WO/2005/090427, filed on March 17, 2005, the disclosure of which is incorporated herein reference. A more detailed DSC and ATREF results are shown below: The DSC curve for the polymer of Example 1 shows a peak with a melting heat of 158.1 J/g of 115-7 ° C melting point (Tm). The corresponding CRYSTAF curve shows the highest peak at 34_5° (with a peak area of 52.9 percent. At 〇5 (:1'!11 and 1' (^813[15 δ is 81.2 °C. The polymer of Example 2 The DSC curve shows a peak with a melting heat of 214.0 J/g at 109.7 ° C melting point (Tm). The corresponding CRYSTAF curve shows that the southernmost bee is at 46.2 C with a 57.0 percent peak area. Between DSC Tm and Tcrystaf ( 5 is 63.5 ° C. 20 The DSC curve of the polymer of Example 3 shows a peak with a melting heat of 160.1 J/g of 120.7 ° C melting point (Tm). The corresponding CRYSTAF curve shows the highest 115 200911847 peak at 66_1 ° ( : and has a peak area of 71.8%. In 〇5 (: D is 111 and butyl (5 is 54.6 ° C between ^ 813 €. The DSC curve of the polymer of Example 4 shows a melting heat of 107.7 J / g of 104.5 The peak of °C melting point (Tm). The corresponding crystAF curve shows that the most 5 peaks are at 30 C and have a 18.2 percent peak area. The ratio between dsc Tm and Tcrystaf is 74.5 ° C. The polymer of Comparative Example A is The DSC curve shows a peak with a melting heat of 86.7 J/g at 90.0 ° C melting point (Tm). The corresponding crystAF curve shows the highest peak at 48.5 ° C with 29.4 The specific peak area. The <5 between DSC Tm and 10 Tcrystaf was 41.8 ° C. The DSC curve of the polymer of Comparative Example B showed a heat of fusion of 129.8.00 J/g of 129.8. (: Melting point (Tm) The corresponding crystAF curve shows the highest peak at 82.2 ° C with a peak area of 83.7 °. The <5 between DSC Tm and Tcrystaf is 47.4 ° C. 15 DSC curve of the polymer of Comparative Example C shows A peak with a melting heat of 145.3 ° C melting point (Tm) of 143.0 OJ/g. The corresponding crystAF curve shows the southernmost peak at 81.8 C with a peak area of 34.7 percent and a lower crystalline peak at 52.4 ° c. The spacing between the two is consistent with the presence of highly crystalline and low crystalline polymers. Between DSCTm and Tcrystaf (5 is 43.5 °C.

20 Examples 5-19, Comparative Example D-F, continuous solution polymerization, catalyst A1/B2 + DEZ was carried out in a computer controlled autoclave reactor equipped with an internal stirrer. Purified mixed-burn solvent (Is〇parTM E from Exx〇nM〇bii Chemical), 2 7 lbs/hr of ethylene (122 116 200911847 kg/hr), 1-octene and hydrogen (when used) It is supplied to a 3.8 L reactor with temperature control and an internal thermocouple clamp. The solvent fed to the reactor was measured by a mass flow meter. A variable speed membrane pump controls the flow rate of the solvent to the pressure regulator. When the pump is discharged, a side flow is taken to provide a flushing flow of the catalyst and the common catalyst i 5 injection line and the reaction agitator. These flows are measured in a Micro-Motion mass flow meter and controlled by a control valve or by manual adjustment of the needle valve. The remaining solvent is combined with 1-octene, ethylene and hydrogen (if used) and fed to the reactor. A mass flow controller is used to transfer hydrogen into the reactor as needed. The solvent/monomer solution temperature was controlled using a heat exchanger before entering the reactor. This stream enters the bottom of the reactor. The catalyst component solution is metered using a pump and mass flow meter and combined with the catalyst flushing solvent and introduced to the bottom of the reactor. The reactor was filled with liquid at 500 psig (3.45 MPa) without vigorous agitation. The product was removed from the outlet line at the top of the reactor. All outlets of the reactor have a small amount of vapor and are insulated. The polymerization is stopped by adding a small amount of water and any hydrating agent or other additive to the outlet line and passing the mixture through a static mixer. The product stream is then heated by passing through a heat exchanger prior to devolatification. This polymer product was recovered by extrusion using a devolverizing extruder and water-cooling the granulator. Details of the process and results are shown in Table 2. Specific polymer properties are included in Table 3. 20 117 200911847 •JJ3 t,[z§] ι^φι^· s day & ^ —5, 6& 铡 啭 C C4e wall 嫛 wcZ3IQZ3IQl-fr$<Ng:l^-氍

Jq/se IV瓌邂 f< 0,901 Γ06 S 卜6-S ΓΗΙ 6.I9I 0-U 9.001 I.IU 6·§ ι,Ι9ε Ι_inch inch s LZL\ε.-Ι L.LSZ 8.9Π •S6

Inch·8 s 0ΊΙ ΓΙΙ •ll •6 3.11 •II 1.11 ΙΊΙ 8.01 8_ol 9ΌΙ 1.11 IH 21 •H •II inch Ό6 e6.s 80,6°°ΗΌ6 ee.s ζ-s S_6S SO6 9S,S IS6 S6 0.06 Γ68 6S 9.6s -0000 6.60° -000°

9ΓΙ 3 SI S Bu I 0-1 I·I 69·! OZ/I 89.1 Α9·1 e9.I Ζ9Ί 09.1 59.1 inch 9Ί sl Δ inch.1 II L9i -e 9〇g - inch s 96£6 inch Z - inch 96S inch% wide L\ SU OG 61 inch 9es so.o OS 5·· Bu 0Ό 60.0 0Γ0s.os,0 0ΙΌ 80Ό JJ ΖΙ·ο el.o 82 9Γ0 ΙΙΌ i -_0

SI OS § e inch - mi ε5 ε inch - §1 e inch 卜 iεκι SI ε inch 卜1 §1 60Ό ΙΓ0 §.0 I inch ΙΌ 01Ό SO 60.0 -.0 6Γ0 i 0Γ0 so ζ-ο ε inch.0 ΔΙ .Ο -*0 ΓΟ 61.0 61.0 90Ό SOO -0 90Ό 0Γ0 •oe inch·οε 60°OSO 17-0 ΖΓΟ inch 1.0 UO -.0 62 90Ό i ΔΙΌ inch ί,ο •oe inch ΙΌ 0.0 90.0 55 01.0 ΟΙΌ寸ΙΌso.o π_0 -ο 9Γ0 π_0 JJ 90.0 ΖΌΌ ΟΙΌ inch ΙΌ 90Ό

L.\L I l l I I Γ I I Γ ru I 卜 U \L \L IL· u U u IL· 0- 3ZI s ΙΠ 3 JJ § 3 I-§ s

00*0 e inch.8Δ 06'9ε ο·- 36.inch s 00-06,6Z •II 6 ·" s.l ze.o 69.0

61 81 ΔΙ 91 - Inch I u ZI ll 01 6 s L 9 *3 *Q -ϊζ^+,ιίί^π260午妹.^-龚^龄--跻恕卜-令阼"-黎装°斗斗 It Crocodile ^哗.9 ^^Ή·^#<0"·ς 5-^^ to §1^^. 璨^^ί4Μ(οΗαπυ-^ί4(砩卜--Μ--'^^^-κ ^^ί^^Ιί^ά--Ι)-^" 燊[(^®-(_-'^f 亚-9)硪-'姝亚--(1^硝肊旁--(^缕婳(^^(^^硪*--1)4-9-)-2].2; 瓛令/". 雔 雔 _W 驷驭畲 4'-two 4 驷粲 '-* 118 200911847 CRYSTAF peak area (percentage), σ\ Os in Os 8 CO ON (N t-H VO (N in ITi (N 5; OO CN On 〇 00 00 TcRYSTAF 1 (°C) 卜 iN T-H CN et m 00 ss 吞 CN OO P ίδ 1 a Η 〇〇g oo r-^ 〇(N m Ο 1- Tc(°C) L jri mf—H »—H 1—HH 〇ί—H sr—H g < N 〇\ § g 5: 〇\ VO On g τ-«Η (N Tm(°C) ! in fN ί—H in H <N iri inch rH cn inch rH (N inch rH 宕in CN melting heat ( j/g) (N cn m 00 T—H g ^T) ^T) 〇〇Ό O CN m (Τ) G\ VO 1—H Mw/Mn 1_ 〇<N 〇(N 13.8 0 (N CN CN (N in 00 00 Η O) 0 (N 0 rj 〇«Ν Os O) Mn (g/m 〇l) 〇OO^ in ^T) 〇rn m 9,980 53,200 53300 53,100 40,100 28700 58,200 36,500 55,100 63,600 0 s 40,100 74,900 〇〇37,900 39,400 Mw (g/mol) 110,000 65,000 137,300 104,600 10960()] 〇1/^ 〇 〇T—H 129,000 1 129600 113,100 66,200 101,500 132,100 81,900 79,900 148,500 107,500 Ο ri ri 76,800 I10/I2 1_ iTi ^0 ir: 13.4 卜 iT) 10 inch vd iTi 〇Os vd i—H 00 〇<5 〇 10.0 [39.0 1 "12.5 00 G\ ^T) (N 卜 ^ 00 a; in 59.2 1 13·2 1 15.6 41.6 inch ro 11.3 24.9 20.3 10 〇〇in 1—H p 0 T—H (N o VO &lt ;N 〇'O d inch on B 0.8627 0.9378 0.8895 0.8786 0.8785 0.8825 0.8828 0.8836 0.8784 0.8818 0.8700 0.8718 0.9116 0.8719 0.8758 0.8757 0.9192 0.9344 xi ω lb l ^Ti 00 σ gt 〇tH rs inch in OO 2 119 200911847 generated aggregate The samples were tested as DSC and ATREF as in the previous examples. The results are as follows: The D S C curve of the polymer of Example 5 shows a peak of a melting point (Tm) of 119.6 ° C with a heat of fusion of 60 °K /g. The corresponding CRYSTAF curve shows that the 5th peak is at 47.6° (: and has a 59.5 percent peak area. At 03 (: D1 and 7/781), 5 is 72.0 ° C. The DSC curve of the polymer of Example 6. A peak of 115.2 ° C melting point (Tm) with a heat of fusion of 60.4 J/g is shown. The corresponding CRYSTAF curve shows a peak at 44.2 ° C with a peak area of 62.7 percent. The d between DSC Tm and Tcrystaf 10 is 71.0. The DSC curve of the polymer of Example 7 shows a peak of 121.3 ° C melting point (Tm) with a heat of fusion of 6 9.1 J/g. The corresponding CRYSTAF curve shows the highest peak at 49.2 ° C with a peak of 39.4 ° The area between DSC Tm and Tcrystaf is 72.1 ° C. 15 The DSC curve of the polymer of Example 8 shows a peak of 123.5 ° C melting point (Tm) with a heat of fusion of 67.9 J/g. Corresponding CRYSTAF curve The highest peak is shown at 80.1 ° C with a peak area of 12.7 percent. The ratio between DSC Tm and Tcrystaf is 43.4 ° C. The DSC curve for the polymer of Example 9 shows a fusion heat of 12.5 ° 20 J / g 12.6 ° The peak of C melting point (Tm). The corresponding CRYSTAF curve shows the highest peak at 80.8 ° C with a peak area of 16.0 percent. In DSC Tm and Tcrys Between taf (5 is 43.8 ° C. The DSC curve of the polymer of Example 10 shows a peak with a melting heat of 6 0.7 J/g of 115.6 ° C melting point (Tm). The corresponding CRYSTAF curve shows the most 120 200911847 The bees were at 40.9 C with a peak area of 52.4 percent. Between dsc Tm and Tcrystaf (5 is 74.7 ° C. The DSC curve for the polymer of Example 11 shows a melting point of 113.6 ° C with a heat of fusion of 70.4 J/g. The peak of (Tm). The corresponding CRYSTAF curve shows the 5th peak at 39.6 ° C with a 25.2 percentage peak area. Between dsc Tm and Tcrystaf (5 is 74.1 ° C. The d SC curve of the polymer of Example 12 shows A peak of melting point (Tm) of 113.2 ° C with a heat of fusion of 4 8.9 J/g. The corresponding iCRYSTAF curve shows no peak or higher than 30 C (Tcrystaf is therefore set at 10 30 ° C for further calculation). Between Tm and Tcrystaf (5 is 83_2. (: The Dsc curve of the polymer of Example 13 shows a peak with a melting heat of 49 4 J/g of 114.4 C melting point (Tm). The corresponding CRYSTAF curve shows the highest peak At 33.8 ° C with a peak area of 7.7 percent. The 5 between the DSCs is 84.4 °C. The DSC curve of the polymer of Example 14 shows a peak of 120.8 C melting point (Tm) having a heat of fusion of 127.9 J/g. The corresponding crystAF curve shows the southernmost peak at 72.9C with a 92.2 percent peak area. Between the DSCs (5 is 47.9 ° C. The DSC curve of the polymer of Example 15 shows a peak with a heat of fusion of 36.2 20 J/g of 114.3 ^ melting point (Tm). The corresponding CRYSTAF curve shows the peak at 32_3 (: and has a 9.8 percent peak area. In 〇 8 (: 7111 and 1 ^ 17 with 讦 (5 is 82.0 ° C. The DSC curve of the polymer of Example 16 shows a heat of fusion of 4 4.9 The peak of the 116.6C melting point (Tm) of J/g. The corresponding CRYSTAF curve shows the highest 121 200911847 peak at 48.0 ° C with a peak area of 65.5 percent. The delta between DSC is 68.6 ° C. The polymer of Example 17 The DSC curve shows a peak of 116.0 ° C melting point (Tm) with a heat of fusion of 4 7 _ 0 J/g. The corresponding CRYSTAF curve shows the 5 peaks at 43.1 C > C and has a peak area of 56.8 percent. Between Tcrystaf (5 is 72.9 ° C. The DSC curve of the polymer of Example 18 shows a peak with a melting heat of 120.5 ° C melting point (Tm) of 丨41.8 J/g. The corresponding crystAF curve shows the highest peak at 70.0 °C with a peak area of 94.0%. The ό between dsc Tm and Tcrystaf 10 is 50.5 ° C. The DSC curve of the polymer of Example 19 shows a melting The heat is the peak of the 124.8 ° C melting point (Tm) of 4.874.8 J/g. The corresponding crystAF curve shows the southernmost peak at 79.9 C with a peak area of 87_9. The δ between DSC Tm and Tcrystaf is 45.0 ° C. 15 The DSC curve for the polymer of Example D shows a peak at a melting point (Tm) of 37.3 ° C with a heat of fusion of 31.6 J/g. The corresponding CRYSTAF curve shows no peak equal to or higher than 300 ° C. These values and densities It is consistent with a low resin. The <5 between DSC Tm and Tcrystaf is 7.3 ° C. The DSC curve of the polymer of Comparative Example E shows a melting point (Tm) of 124.0 ° C with a heat of fusion of 20 179.3 J/g. The corresponding CRYSTAF curve shows the highest peak at 79.3 ° C and has a 94.6% percent peak area. These values are consistent with the higher density resin. The ratio between DSC Tm and Tcrystaf is 44.6 ° C. Comparative Example The DSC curve of the polymer of F shows a peak of 124.8 ° C melting point (Tm) with a heat of fusion of 90.4 J/g. The corresponding CRYSTAF curve shows that the peak is at 77.6 ° C and has a peak area of 19.5 percent. The separation between the two peaks is consistent with the presence of south crystalline and low crystalline polymers. In DSC Tm with

The delta between Tcrystaf is 47.2. (3. Physical property test 5 Polymer samples for physical property evaluation, such as high temperature resistance properties such as temperature test, particle retardation strength, high temperature recovery, high temperature compressive strain and storage modulus ratio, 0, (25. 〇 / 〇 (100. 〇 Description. Several commercially available polymers were included in the test: Comparative Example G* is a substantially linear ethylene octene copolymer (AFFINITY®, available from The Dow Chemical Company), comparing 10 examples An elastic, substantially linear ethylene/:[_octene copolymer (AFFINITY® EG8100, available from The Dow Chemical Company), Comparative Example I is a substantially linear ethylene/1-octene copolymer (AFFINITY® PL1840, by Comparative Example J is a hydrogenated styrene/butadiene/styrene triblock copolymer (KRATONTM G1652, available from KRATON Polymer 15), and Comparative Example K is a thermoplastic sulfide. (TPV, a polyolefin blend containing a crosslinked elastomer dispersed therebetween). The results are presented in Table 4. Table 4 High Temperature Mechanical Properties Example TMA-lmm Penetration ro Particle Blocking Strength lb/ft2 (kPa) G , (25 ° C) / G (100 ° C) 3 00% strain recovery (80 ° C) (percent) Compressive strain (70 ° 〇 (percent) D * 51 - 9 failure - E* 130 - 18 - - P* 70 141 (6.8) 9 failure 100 5 104 〇(〇) 6 81 49 6 110 - 5 - 52 7 113 - 4 84 43 8 111 - 4 Failure 41 9 97 - 4 - 66 10 108 - 5 81 55 123 200911847 11 100 - 8 - 68 12 88 - 8 - 79 13 95 - 6 84 71 14 125 - 7 - - 15 96 - 5 - 58 16 113 - 4 - 42 17 108 〇(〇) 4 82 47 18 125 - 10 - - 19 133 - 9 - - G * 75 463(22.2) 89 Failure 100 H* 70 213 (10.2 29 Failure 100 I* 111 - 11 - - J* 107 - 5 Failure 100 K* 152 - 3 - 40 In Table 4, compare Example F (use The physical blend of the two polymers of the simultaneous polymerization of the catalysts A1 and B1 has a 1 mm penetration temperature of about 70 ° C, while the examples 5-9 have a 1 mm penetration of 100 ° C or more. Permeability temperature. Further, Examples 10-19 all have a 1 mm penetration temperature of 5 degrees greater than 85 ° C, and most have a 1 mm TMA temperature greater than 90 ° C or greater than 10 ° C. This shows that the multi-block polymer has a better dimensional stability at a higher temperature than the physical blend. Comparative Example J (a commercial SEBS) has a good 1 mm TMA temperature of about 107 ° C, but it has a very poor compressive strain of about 100 percent (high temperature 70 ° C), with a 300 percentage at high temperature (80 ° C). 10 The response is invalid when the change is made (the sample is broken). Thus, the exemplified polymers have a unique combination of properties that are not available in commercially available high performance thermoplastic elastomers. Similarly, Table 4 shows a multi-block polymer with a low (good) storage modulus ratio of G or less (25 ° C) / G' (100 ° C) of 6 or less, while a physical blend (comparison 124 200911847 Example F) A random ethylene/octene copolymer having a storage modulus ratio of 9 and a similar density (Comparative Example G) has a larger storage amount ratio (89). It is expected that the polymer storage modulus ratio is as close as possible to 〗. This polymer will be relatively unaffected by temperature, and thus articles made from the polymer can be used at - wide temperature. This low-storage Wei Guan and temperature I correlation is available for Kate, such as in pressure sensitive bonding formulations. 10 15 The data in Table 4 also illustrates that the multi-block polymers of the present invention have good particle retarding strength. In particular, Example 5 has a particle retarding strength 1 of crepe paper which means that it is relatively free flowing under the conditions tested, compared to what is shown to be quite agglomerated: F and G'. The retardation strength is important because polymers having a large resistance π strength cause agglomeration or purity of the product upon storage or transportation in a large amount of transportation, resulting in poor handling properties. The high temperature (10) compressive strain of the 2 multi-block polymer is generally good, typically less than about 80 percent, preferably less than about 70 percent, and especially about 6 percent. Conversely, the comparative examples, G, Η and ; all have a compression strain of 7 百分比 0% (the maximum possible value, showing no recovery). Good high temperature seam change (low number of materials, window profile, 〇-% and the application of similar applications. 125 09 200 7 84 itr%os 念 oe

OS (^φκπ) 粼一r 趔οο ι i 13⁄4 '-N ΤΓΤΓNNNΤΓMM 1^, a ΤΓ ίτ7Γ oe (Bdeirir 鹚%0SI念 09£ 09卜 018 I9S 06b 00 inch

, o1-1 09S 0Z6 OS i 0-1 ose Oil 0061 连 ^_%00ε513⁄4 s inch /, ΎΓNN 1^1 1^, s121 ^1 09 96 (qJLi^s.)^ ^»w%001513⁄4 16

L%~^L s 1^, 16 1^, "W" ei "(4) L% e6 (fs) α 4 4 6ee 19 inch 169 §1—9L61 inch § inch s 69S 9 inch (UIUI) Vs 婼韬:ΐί-dian (%) w*^^ inch ΖΌΙ s 609 L69 6Nn 0001 un _ S6es SSI ss ie6 0601 i011°°1 KS lsole6 9ΠΙ§ 3⁄43⁄4 (%) 3⁄4^3⁄4 3⁄43⁄4 0§) Engage鹚4 transport fel^ 6rl SI T" 9e oei i" π SI 6Z π ei 9ΐ inch i inch I-inch i inch i 91 31 6SI 01 ie IS6 inch ι sz, 9 inch 8 n ΤΓ 196

SI π π s -' '- £8 inch 6 £ Ζ 81 0n inch I 091 inch T~ 卜一 se s called Li 6N inch Z 9 inch 6S5 OIZ 91 1-1 — eze oz ~ il SI HM 9" 0 £ Uz en i inch inch oe IS S68 π curry, '-¥^ρ8ε^ ^f-^uis/m.^

*fc *3 *Q *1N *o ΤΓN N ΤΓN ΤΓ ΤΓNN (4) 126 200911847 Table 5 shows the mechanical properties of the new polymer and various comparative polymers at room temperature. It can be seen that multi-block polymers have very good abrasion resistance when tested according to IS0 4649, typically exhibiting a volume loss of less than about 90 mm3, preferably less than about 80 mm3, and especially less than about 50 mm3. . The higher value in this test 5 indicates a higher volume loss and thus a lower anti-wear property. The tear strength is determined by the tensile notch tear strength of the olefin multi-block polymer, which is usually 1000 mJ or more, as shown in Table 5. The tear strength of the olefin multi-block polymer can be as high as 3000 mJ, or even as high as 5000 mJ. The polymers of the comparative examples typically have a tear strength of no more than 750 mJ. 10 Table 5 also shows that the multi-block polymers of the present invention have better shrinkage stress (illustrated by higher shrinkage stress values) at 150% strain than some of the comparative examples. Comparative Examples F, G, and Η have a shrinkage stress value of 400 kPa or less at 150 percent strain, while the olefin multi-block polymer has a shrinkage stress value of 5 kPa at 150 percent strain (Example 11). Approximately 15 1100 kpa (Example 17) is high. Polymers having a higher value than the 150 percent shrinkage stress will be particularly suitable for elastic applications such as elastic fibers and fabrics, especially non-woven fabrics. Other applications include diapers, physiology, and medical clothing, wristband applications such as signage and elastic bandages. Table 5 also shows that the stress relaxation (at 50 percent 20 strain) of the olefin multi-block polymer has also been improved (less) compared to, for example, Comparative Example G. Lower stress looseness means that the polymer retains more force in the application, such as diapers, which require a long time to retain their elastic properties at body temperature. The monoolefin multi-block heteropolymer, and preferably the ethylene/ruthenium multi-embedded heteropolymer, may comprise a combination of at least two embodiments as described herein. 127 200911847 In another embodiment, a blend of at least, for example, an olefin polymer as described herein and at least one olefin multi-block heteropolymer such as described herein can be used. In another embodiment, an ethylene-based polymer as described herein can be blended with an olefin multi-block heteropolymer as described herein. In another embodiment, a propylene-based polymer as described herein can be blended with an olefin multi-block heteropolymer as described herein. In another embodiment, an ethylene-based polymer as described herein, and a propylene-based polymer as described herein, can be blended with an olefinic multi-block copolymer as described herein. The thermoplastic polyurethane may optionally be used in the composition of the polyurethane component of the composition with respect to its formulation, except that it is required to be thermoplastic in nature, which means that it is prepared from a substantially difunctional component. For example, an organic diisocyanate and a component which is substantially difunctional with an active 15 hydrogen group. However, in some cases, a small amount of a component having a functionality higher than two may be used. This is particularly suitable when an extender such as glycerin, trishydroxypropane, and the like are used. This thermoplastic polyurethane composition is generally referred to as a TPU material. Accordingly, any TPU material known in the art can be used in the compositions of the present invention. For a representative teaching of the preparation of TPU material 20, see Polyurethane: Chemistry and Technology, Part II, Saunders and Frisch, 1964, pp. 767-769, New York, NY, USA, Interscience Publishing Company, New York, NY, USA Hanser Publications, Inc., published by Macmillan Publishing Company, Polyurethane 128 200911847

Handbook, 1985, edited by G. Oertel, pp. 405-417. Specific teachings of various TPU materials and their preparation can be found in U.S. Patent Nos. 2,929,800, 2,948,691, 3,493,634, 3,620,905, 3,642,964, 3,963,679, 4,131,604, 4,169,196, Re 31,671, 4,245,081, 5,371,684, 4,379,904, 4,447,590, 4,523,005, 4,621,113, and 4,631,329; The full text of these patents is incorporated into this case for reference. Preferably, the TPU is a polymer prepared from a mixture comprising an organic diisocyanate, at least a polymerized alcohol, and at least a monofunctional extender. This TPU can be prepared by a prepolymer, a quasi-prepolymer, or a one-stage process incorporating the method of Reference 10 herein. Di-isocyanates suitable for use in the hard segment of the present invention for preparing polyaminophthalic acid esters include combinations of aromatic, aliphatic, and cycloaliphatic di-isocyanates with at least two of such compounds. An example of a structural early element derived from a di-isocyanate (〇CN_R_NC〇) is given by the following chemical formula (I): 0 π II 9 —c~~HN-R-nh—C— m 15 (1), wherein R is a dilute group , cycloalkenyl or aralkenyl. Representative examples of such bis-isocyanates can be found in U.S. Patent Nos. 4,385,133, 4,522,975 and 5,167,899. Preferably, the isocyanate vinegar comprises but is not limited to 4,4,_di-isocyanodecyldiphenyl decane, p-phenylene diisocyanate, hydrazine, 3 bisisocyanyl 20 fluorenyl hydrazine Base)-cyclohexane, 1,4-di-isocyanodecyl-cyclohexane, hexamethylene di-isocyanate, 1,5-naphthalene diisocyanate, 3,3,_dimethyl Base_4,4ι·bisphenyldi-isocyanate, 4,4′-di-isocyanodecyl-dicyclohexylmethane, and 2,4-toluene diisocyanate. More preferably, it is 44,_di-isocyanodecyl-dicyclohexyldecane and 4,4,- 129 200911847 di-isocyanoguanidino-diphenylmethane. A preferred one is 4,4'-di-isocyanodecyldiphenylmethane. Di-isocyanates also include family and cycloaliphatic isocyanate compounds such as 1,6-hexamethylene-di-isocyanate; ethylene di-isocyanate; 1-isocyanoquinone 5yl-3,5,5-trimethyl- 1-3-isocyanatomethylcyclohexane; 2,4- and 2,6-hexahydrotoluene di-isocyanate, and corresponding isomer mixtures; 4,4'-, 2,2'- and 2,4'-Dicyclohexyl-decane di-isocyanate, and the corresponding mixture of isomers. Further, 1,3-tetramethylene xylene diisocyanate can also be used in the present invention. The isocyanate may be selected from the group consisting of organic isocyanates, modified isocyanates, 10 isocyanate prepolymers, and mixtures of at least two of such isocyanates. Any organic diisocyanate previously used in the preparation of TPU can be used, including mixtures of aromatic, aliphatic, and cycloaliphatic diisocyanates with the like. Illustrative isocyanates include, but are not limited to, methylene bisphenyl isocyanate, including 4,4'-isomers, 2,4'-isomers, and mixtures thereof; m- and p-phenylenes 15 bases Isocyanate; chlorophenylene diisocyanate; α,α'-p-xylene diisocyanate; 2,4- and 2,6-toluene diisocyanate and a mixture of the latter, which are commercially available; Toluidine diisocyanate; hexamethylene diisocyanate; 1,5-naphthalene diisocyanate; isophorone diisocyanate and the like; cycloaliphatic diisocyanate, such as methylene dicyclohexyl 20 isocyanate, including a 4,4'-isomer, a 2,4'-isomer, a mixture thereof, and the like, and all geometric isomers thereof, including trans/reverse, cis/trans, cis/cis, and the like a mixture; cyclohexenyl diisocyanate (1,2-; 1,3-; or 1,4-); 1-mercapto-2,5-cyclohexyl diisocyanate; 1-methyl-2, 4-cyclohexenyl diisocyanate; 1-mercapto-2,6-cyclohexenyl diisocyanate; 4,4'-isopropylidene double 130 200911847 - (cyclohexyl isocyanate); 4, 4'- Isocyanato Hexyl, and the like geometrical isomers and any mixtures of the like. Also included is a modified form of methylene bis(phenyl isocyanate). The latter means that such forms of fluorenyl bis(phenyl isocyanate) have been treated to stabilize the liquid at room temperature (about 20 ° C). Such products include those which have been reacted with a minor amount (up to about 0.2 equivalents per equivalent of polyisocyanate) of a mixture of aliphatic diols or aliphatic diols as described in U.S. Patent Nos. 3,394,164; 3,644,457; 3,883,571; 4,031,026; 4,115,429; Modified fluorenyl bis(phenyl isocyanate) of 4,118,411; ^4,299,347; each of which is incorporated herein by reference. The modified methylene bis(phenyl isocyanate) also includes a carbodiimide that has been treated to convert a small amount of diisocyanate to the corresponding carbodiimide, which in turn interacts with the re-diisocyanate to form a urethane-imidolong, which is formed. The product is a stable liquid at room temperature, as described in U.S. Patent No. 3,384,653, the disclosure of which is incorporated herein by reference. If desired, a mixture of the above identified polyisocyanates of 15 can be used. Suitable organic diisocyanate families include aromatic and cycloaliphatic diisocyanates. Preferred species in such families are methylene bis(phenyl isocyanate) and include mixtures of 4,4'-isomers, 2,4'-isomers, and the like, and methylene bis ( Cyclohexyl isocyanate) and includes the aforementioned isomers. In a preferred embodiment 20, the isocyanate is a mixture of 1,3-bis(isocyanatomethyl)cyclohexane and 1,4-bis(isocyanomethyl)cyclohexane. In still another embodiment, the diisocyanates are present in a weight ratio of about 1 to 1. Polymeric diols which can be used include those well known in the art for use in TPU elastomer preparation. The polymeric diol is responsible for the formation of soft segments in the resulting polymer, and 131 200911847 preferably has a molecular weight (number average) between 200 and 10,000 g/mol range, preferably between 400 and 4,000 g. / Mohr range 'and more preferably from 5 〇〇 to 3,000 g / m. Typically and in some instances, it may be advantageous to use at least one polymeric diol. Examples of such diols are polyether diols, poly-branched diols, 5-based-terminated polycarbonates, base-terminated polybutadienes, and trans-terminated polybutadiene-acrylonitriles. a copolymer, a dialkyl siloxane, and a hydroxy-terminated copolymer of alkylene oxide, such as ethylene oxide, propylene oxide, and the like, and mixtures thereof, wherein any of the foregoing polyols is used As the main component (greater than 10 50% w/w) with the amine-terminated polyether and the amine-terminated polybutadiene-acrylonitrile copolymer. Other examples of diols include natural oil diols. Suitable polyether polyols include polyoxyethylene glycol, polyoxypropylene glycol, which are optionally blocked with an ethylene oxide residue; random and smothered copolymers of ethylene oxide and propylene oxide; a polytetramethylene glycol; a random and block copolymer of tetrahydrofuran with ethylene bromide and/or propylene oxide; and a carboxylic acid of any of the foregoing and -15 functional groups and derived from the acid The ester-derived product, in the latter case, undergoes transesterification and the esterification group is substituted with a polyether diol group. Preferred polyether polyols are random and block copolymers of ethylene and a polytetramethylene glycol polymer having a functionality of about 2 Å and a polytetramethylene glycol having a functionality of about 2.0. Suitable polylactic acid polyols include those obtained by polymerizing ε-caprolactone using an initiator such as ethylene glycol, ethanolamine and the like; and by polyols such as ethylene glycol, butane diol, % Benzene-methanol and its likes are prepared from polycarboxylic acids such as phthalic acid, terephthalic acid, succinic acid, glutaric acid, adipic acid, sebacic acid and the like. By. 132 200911847 Suitable amine-terminated polyethers are aliphatic primary diamines derived from polyoxypropylene glycol structures. This type of polydiamine is commercially available from Jefferson Chemical under the trade name JEFF AMINE (now available from Basell). Suitable hydroxy-containing polycarbonates include those obtained by reacting a diol with a diaryl carbonate or with 5 phosgene, such as propane-1,3-diol, butan-1, 4-diol. , hexane-1,6-diol, 1,9-decanediol, 2-methyloctane_ι,8·diol, monoethyl alcohol, diethylene glycol, dipropylene glycol and the like , a diaryl carbonate such as diphenyl carbonate.

Suitable ruthenium-containing polyethers include copolymers of alkylene oxide and dialkyl decane, and the like, and the like, and the like (see, for example, 'US Patent No. 4,057,595' Or the aforementioned U.S. Patent No. 4,631,329, the disclosure of which is incorporated herein by reference. Suitable hydroxy-terminated polybutadiene copolymers include Arc 〇

A compound obtained by Chemical Company under the trade name Poly BD Liquid Resin. The hydroxy- 15 alkyl t-dilute copolymer is also available from Sartomer. The base- and amine-terminated butadiene/acrylonitrile copolymers are described as materials obtainable from the trade names hycar hydroxy-terminated (HT) liquid polymer and amine-terminated (AT) liquid polymer, respectively. Preferred diols are the aforementioned polyethers and polyester diols. Difunctional extenders which may be used may be any of those known in the foregoing disclosure. Basically, the extender may be an aliphatic straight chain and branched chain diol having from 2 to 1 Torr of carbon atoms in the chain. The description of the diol is ethanol, 1,3-propanediol, 1,4-butanediol, terpene diol, "-hexane alcohol, neopentyl glycol, and the like; M• ring Diethanol, p-benzene 1,3_ and 1,2-isomers, iso-p-bis(light)ethyl ether; cyclohexanediol (1,4_ 133 200911847 propylene bis-decyl alcohol) , diethylene glycol, dipropylene glycol, ethanolamine, N-methyl-monoethanolamine, and the like; and mixtures of any of the foregoing. As previously mentioned, in some instances, a minor portion of the difunctional extender Parts (less than about 20 equivalent percent) are replaced by a trifunctional extender without reducing the thermoplasticity of the formation of τρυ 5; the description of the extender is glycerol, trishydroxypropane, and the like. Although the foregoing description and illustration Any of the glycol extenders may be used singly or as a blend, preferably using 1,4-butanediol, i,6-hexanediol, neopentyl glycol, 1,4-cyclohexane Methanol, ethylene glycol, and diethylene glycol, which may be used alone or in admixture with each other or with at least one of the previously mentioned aliphatic diols. 1,4-butanediol, 1,6-hexanediol and j,4-cyclohexanedimethanol. The chain extension dose of the incorporated polyurethane is selected by the specific reactant component, The amount of hard and soft segments, and the 15 index sufficient to provide good mechanical properties such as modulus and tear strength. The polyurethane composition used in the practice of the present invention may contain from 2 to 25 wt% of the chain. The extender component, preferably from 3 to 20% by weight of the chain extender component and more preferably from 4 to 18% by weight of the chain extender component. If desired, a small amount of mono-based functional group or single Amino functional group compounds, commonly referred to as "chain stoppers," are used to control the amount of molecule 20. The description of the chain stopper is propanol, butanol, pentanol and hexanol. When used, the chain stop agent is present substantially in a trace amount of from 01 to 2 weight percent of the reaction mixture which results in a polyurethane composition. The equivalent ratio of the V-alcohol to the extender can be varied depending on the hardness expected from the TPU product. In general, the ratio falls between about 1 : i to about J: 134 200911847 20, preferably between about 1: 2 and about 1: between. At the same time, the total ratio of the isocyanate equivalent to the equivalent weight of the active hydrogen-containing material is in the range of 0.90:1 to 1·ΐ〇:1, and preferably 0.95:1 to 1.05:1. The TPU forming component can be reacted in an organic solvent, but is preferably reacted in an insoluble solvent at about 125. (: melt-pressure at a temperature of about 250 ° C, preferably extruded at about 225 ° C at about 160 ° C. It is generally necessary, but not necessary, to include a catalyst in the reaction mixture to prepare the compositions of the present invention. Any of the catalysts which are conventionally used in the art for catalyzing the reaction of isocyanates with reactive hydrogen-containing compounds can be used for this purpose; see, for example, Saunders et al, Polyurethanes, Chemistry and Technology, Part I, Interscience, New York, 1963, pp. 228-232; also refers to Britain et al., J_Applied Polymer Science, 4, 207-211, 1960; the disclosures of which are incorporated herein by reference. , tin, iron, record, shaft, brocade, miao, stove, Ming, 15 mercury, zinc, nickel, antimony, molybdenum, vanadium, copper, manganese and strontium organic and inorganic acid salts and organometallic derivatives, and scales and three Organic amines. Representative organic catalysts are tin octoate, tin oleate, tin dibutyl dioctoate, tin dibutyl dilaurate, and the like. Representative tertiary organic amine catalysts are three. Ethylamine; triethylenediamine; Ν, Ν, Ν', Ν'- Methyl ethylene diamine; ν, Ν, Ν ', Ν'-tetraethyl 20-ethyl ethanediamine, hydrazine-methyl hydrazine; hydrazine-ethyl phenanthrene; ν, Ν, Ν, Ν, - Tetramethyl hydrazine; hydrazine, hydrazine, hydrazine, Ν'-tetramethyl-1,3-butanediamine; hydrazine, hydrazine-dimethylethanolamine; hydrazine, hydrazine-diethylethanolamine and the like. The amount of catalyst used is typically in the range of from about 0.02 to about 2.0 weight percent of the total weight of the reactants. As discussed above, the polyurethane vinegar can be mixed by virtually all of the wounds in the first-order 135 200911847 process. The wounding may be prepared by stepwise adding a component in a "prepolymerization process" which may be carried out in the presence of optional additives or without the addition of optional additives. The polyurethane formation The reaction can occur in agglomerates or in solution with or without the addition of a catalyst suitable to promote the reaction of the isocyanate with the hydroxyl group or its 5 gram group. An exemplary preparation of such polyurethanes is exemplified in U.S. Patent No. 5,864, 〇〇1. As for the article, the other major components of the hard segment of the present invention are at least one chain. Long agents, which are known in the art. As is known from 10, when the chain extender is a diol, the resulting product is a thermoplastic polyurethane urethane (TPU). When the chain extender is a diamine Or an amino alcohol, the resulting product is technically a thermoplastic polyurea (TPUU). The chain extender useful in the present invention is characterized by two or more guana b groups, preferably difunctional groups, each The functional group contains an "active hydrogen atom." The di-glycol group is preferably in the form of a hydroxyl group, a primary amine group, a secondary amine group, or a mixture of at least two of these groups. The term "active hydrogen atom" refers to the activity of a hydrogen atom by the Zerewitinoff test due to its position in the molecule, which is described in Kohler in j. Am. Chemical Soc., 49, 31-81 (1927). The 2q bond length agent may be aliphatic, cycloaliphatic, or aromatic and is exemplified as a diol, an amine, and an amino alcohol. An illustrative example of a difunctional chain extender is ethylene glycol, ethylene glycol, Propylene glycol, dipropylene glycol, 1,3-propanediol, 1,3-butane monool, 1,4-butanediol, hydrazine, 5-pentanediol and other pentanediol, 2-ethyl- 1,3-hexanediol, 2-ethyl-16 hexanediol, other 2-ethyl-hexyl 136 200911847 diol, 1,6-hexane diol and other hexane diol, 2, 2,4_trimethylpentane-1,3-diol, decanediol, dodecanediol, bisphenol A, hydrogenated bisphenol a, 1,4-cyclohexanediol, bismuth-double 2-hydroxyethoxy)-cyclohexane, u-cyclohexanedimethanol, 1,4-cyclohexanediol, 1,4-bis 2-hydroxyethoxy)benzene, ester diol 5 204 ( Propionic acid, 3_hydroxy-2,2-dimethyl] _3_hydroxy~2,2-dimethylpropyl ester, N-methylethanolamine, available from TCI America N-methyliso-propylamine, 4-aminocyclohexanol, 1,2-diaminoethane, hydrazine, 3-diaminopropane, monoethylenediamine, toluene-2,4_ Diamine and toluene _ 丨, 6-diamine. It is preferably an aliphatic compound containing 2 (up to 8 carbon atoms). If a thermoplastic or soluble polyamine decanoic acid 10 ester is produced, the chain extender is two in nature. Functional groups. Amine chain extenders include, but are not limited to, ethylene diamine, monosterolamine, and propylene diamine. Generally used linear chain extenders are typically diols, diamines or amine alcohol compounds which are characterized by having Molecular weight greater than 400 g/mol (or dow). As used herein, "linear" means not including a branch of tertiary carbon. 15 Examples of suitable chain extenders are those represented by the following structural formula: HO_( CH2)n-〇H, H2N-(CH2)n-NH2 and H2N-(CH2)n-OH, wherein "n, I is substantially a number from 1 to 50. A common chain extender is 1,4 Butanediol ("butanediol," or "BDO")' is represented by the following chemical formula: h〇_CH2Ch2CH2CH2-OH. 20 Other suitable bond extenders include ethylene glycol; diethylene glycol; , 3-propanediol '1,6-hexanediol; 1,5-heptanediol; triethylene glycol; i, 2-ethylhexenyl alcohol (EHD diol); and at least two of these extenders In one embodiment, the chain extender is 1,2-ethylhexene diol (EHD diol). The ring bond extender of the diol, diamine or amino alcohol compound is also suitable for use. 200911847::: Signs are molecules with a molecular weight of no more than 4〇〇g/_ (or Dow). As used herein, "ring," refers to a ring structure, and is exemplified but not limited to a 5 to 8 membered ring having a base-alkyl group 4 = 5 10 15 =: _ _ table... II, = - The ring has two fluorenes wherein 'a 1 to 5 carbon alkyl chain, and each:: is all carbon. In these examples, the end group -0H or - can be substituted by P. Suitable ring dimethanol ("Caf M,, —: End 2 He _== Preferably ΓοΓ(4)' The structural unit of CHDM is π chemical formula: HO-CH2·(cyclohexene)_Ch2_〇h. Chain extender is incorporated into polyurethane vinegar The amount of mechanical, such as modulus and tear strength, is selected by the specific reactant group, the amount of hard and soft segments, and the index sufficient to provide (iv) mechanical properties. The carbamate composition may contain from 2 to 25 wt% of the chaining agent component, preferably from 3 to 20% by weight, of the chain extender component and more preferably 〇wt% of the chain extender component. Alternatively, a small amount of a mono- or tri-amino-functional compound 'it is often referred to as a "chain stopper" to control the molecular weight. Examples of chain-stopping agents are propanol, butanol, pentanol, And hexanol. When a chain stop 20 is used, it is present substantially in an amount which is from 0.1 to 2 wt% of the reaction mixture which results in the polyurethane carboxylic acid composition. As is known to those skilled in the art, The ratio of isocyanurate to total functional groups determines the η of the polymer. In some instances, it requires the use of very small excesses of isocyanate. 138 200911847 For linear, high Μη polymers, it is necessary to have a difunctional group per chain. The starting material. However, it can be adapted to a variety of starting materials having a range of functional groups. For example, a polydiene having a functional end can be used to block the intermediate portion of the repeating isocyanate-chain extender group. Polyurethane. The two ends of the ester. Polydiene having more than difunctional groups can form branched polymers. Although if the functionality is too high, there may be problems of crosslinking and gelation, but usually controlled by process conditions. This branched polymer can exhibit the rheological properties required in some examples, such as high melt strength. (As discussed above, the selective use in the formulation promotes or enhances the formation of 10 urethane groups. Examples of effective catalysts are tin octoate, dibutyltin dilaurate, tin oleate, tetrabutyltin titanate, tributyltin chloride, cobalt naphthalate, dibutyltin oxide, potassium oxide. , tin chloride, ruthenium, osmium, iridium, Ν'-tetramethyl-1,3-butanediamine, bis[2-(oxime, Ν-dimethylamino)ethyl]ether, 1,4 -Diazabicyclo[2.2.2]octanoate; zirconium chelate, aluminum chelate and 15 hydrazine carbonate. When used as a catalyst, the amount of catalyst used is basically in the case of polyamine ruthenic acid, S 0.001 wt% or less to 2 wt% and more of the total amount of the constituent components. I may be used to modify the properties of the polyaminophthalic acid ester of the present invention using an additive. The additive may be used for this technique. Traditional usage known in the field and literature. Typically, the additives are intended to provide the desired properties of the polyurethane, such as various antioxidants, UV inhibitors, waxes, thickeners, and fillers. When a filler is used, it may be organic or inorganic, but usually inorganic such as clay, talc, calcium carbonate, cerium oxide, and the like. Also, fiber additives such as glass or carbon fibers may be added to impart specific properties. The polyurethane used in the practice of the present invention is preferably prepared by reacting a functional poly(139 200911847) ester with an isocyanate and optionally a hydrazine extender. In the 'prepolymer" process, substantially at least one functional polydiene can be reacted with at least one isocyanate to form a prepolymer. The prepolymer is further reacted with at least one chain extender. Alternatively, the polyamino phthalate can be prepared by a 5-stage reaction of all of the reactants. Typical polyurethanes have a number average molecular weight of from 5,000 to 1, 〇〇〇, 〇〇〇 g/mo, and more preferably from 2 〇 to 1 〇〇 / g/mol. In a preferred embodiment of the invention, the polyurethane is formed from a polyester, an isocyanate, and a chain extender, and is preferably an aliphatic chain extender. In the preferred embodiment, the polyesters have at least one ester group in the molecule, and preferably at least a diester group, and have substantially 5 Å to 1 Å, 〇〇〇iMn, preferably 1,000 to 5,000 and more preferably 1,000 to 3 〇〇〇g/m〇1. In another embodiment t, the polyurethane is formed from a composition comprising: 10 to 40 wt% of di-isocyanate, preferably 15 to 35 15 wt% of di-isocyanate; 50 to 85 The wt% polyester, preferably 55 to 80 wt% of the polyacetate' and more preferably 6 to 8 wt% of the polyacetic acid; and 2 to 15 wt% of the chain extender, preferably 2 to 1% by weight of chain extender (each weight percentage is based on the total weight of the reactants). In still another embodiment, the di-isocyanate is an aliphatic or aromatic diisocyanate, and more preferably 4,4, diphenylmethanedioxane diisocyanate. In still another embodiment, the chain extender is an aliphatic diol. In still another embodiment, the polydiene diol has a 〇〇η of 5〇〇 to 1〇〇〇〇g/m〇1, preferably 1,000 to 5 〇〇〇g/m 〇]iMn and more preferably 〗, 5 〇〇 to 3,000 g / mol Μ η. In one embodiment, the polyurethane has a density greater than or equal to 〇9〇140 200911847 g/cc, preferably greater than or equal to 〇, 95 g/cc, and more preferably greater than or equal to 1.00 g. /cc. In another embodiment, the polyamino decanoic acid s is intended to have a density of 1.30 g/cc or less, preferably less than or equal to 丨25 g/ee, more preferably less than or equal to 1.20. g/cc. In another embodiment, the polyamine oxime ester has a density of from 0.90 g/cc to 1.30 g/cc, preferably 〇 95

s' 1C to 1_25 g/cc density, and more preferably 1.00 g/cc to 1.20 g/cc of murmur from 0_90 g/cc to 1.30 g/cc, all individual values and sub-ranges are included and disclosed In the present invention. f In another embodiment, the polyurethane has a melt index greater than or equal to 〇 10 g/10 min, preferably greater than or equal to 0.2 g/ιο divided, and more preferably greater than Or equal to 0.5 g / ΙΟ minutes, and most preferably greater than or equal g / ΙΟ minutes (ASTM D-1238-04, 190 ° C, 8.7 kg). In another embodiment, the polyurethane has a martenid index of less than or equal to 100 g/10 minutes, preferably less than or equal to 50 g/min, more preferably less. It is equal to or equal to 15 20 g/min, and is preferably less than or equal to 10 g/1 min (Ast^ D-1238-04 '230 ° C, 8.7 kg). In another embodiment, the polyaminomethyl' acid ester has a melt index of from 0.1 g/10 min to 1 g/l〇, preferably from 0.5 g/ΙΟ min to 50 g/l min. More preferably, it is 1 g/i 〇 minute to 2 〇 g/i 〇 eight minutes, and most preferably 1 g / ΙΟ minute to 1 〇 g / l 〇 minutes. In a preferred embodiment 20, the polyurethane has a melt index of from 6 g/Torr to 10 g/l, preferably from 7 g/l min to 9 g/μ min. All individual values and sub-ranges from gg/1〇 to 1〇〇g/10 min are included and disclosed in the present invention. Preferred polyurethanes include PELLETHANETM thermoplastic polyurethane elastomers from The Dow Chemical Company. 141 200911847 Other polyamino phthalates useful in the present invention include, but are not limited to, ESTANE thermoplastic polyurethanes, TECOFLEX thermoplastic polyamino phthalates, CARBOTHANE thermoplastic polyamino phthalates, TECOPHILIC thermoplastic polyamines The phthalic acid ester, TECOPLAST thermoplastic poly-5 urethane and TECOTHANE thermoplastic polyamino phthalate, all of which are available from Noveon; ELASTOLLAN thermoplastic polyurethanes from BASF and other thermoplastic polyamines Carbamates; and thermoplastic polyurethanes commercially available from Bayer, Huntsman, and Merquinsa. The polyurethane vinegar component may contain a combination of at least two of the foregoing suitable embodiments. If desired, the polyamino phthalate may incorporate additives such as pigments, fillers, lubricants, stabilizers, antioxidants, dyes, flame retardants, and the like at any convenient stage of preparation, such as general and poly The urethane elastomers are used together. 15 Filler One of the compositions of the present invention may comprise at least a filler. Such fillers include, but are not limited to, citrate, aluminate, aluminum silicate, alumina, talc, mica, carbonate, titanium dioxide, and magnesium hydroxide. Fillers also include surface modified fillers including, but not limited to, surface modified cerium oxide and surface modified bismuth phthalate (preferably talc). In one embodiment, the filler is a citrate which is surface modified with hydroxydecane. In another embodiment, the filler is a talc which is modified with a surface of the geminite. In another embodiment, the filler is a monocaprate, which is surface modified with an amino decane 142 200911847. In another embodiment, the filler is a talc that is modified with an amino decane surface. In another embodiment, the amino decane is selected from the group consisting of: R2 R1-Si-NH2

R3 R2 R4 R1- Si-〇 -Si -NH2 (II), R3 R5

R2 R6

(III)

5 For the structural formula I, each of iU, R2 and R3 is independently an alkyl group (preferably methyl or ethyl), hydrogen, or chlorine. For Structural Formula II, each of R1, R2, R3, R4 and R5 is independently an alkyl group (preferably methyl or ethyl), hydrogen, or chlorine. For the structural formula III, each of 10 IU, R2, R3, R4, R5, R6 and R7 is independently an alkyl group (preferably methyl or ethyl), hydrogen, or chlorine, and η is 0 to 50. It is preferably from 0 to 20, and more preferably from 0 to 10. In another embodiment, the composition of the present invention comprises from 0 143 200911847 to 60 weight percent of the total weight of the composition, preferably from 5 to 5 weight percent, and more preferably from 10 to 40 weight percent. In yet another embodiment, the filler is a citrate. In another embodiment, the filler is a talc. In another embodiment, the filler is a citrate which is modified with an amino decane surface. In another embodiment of 5, the filler is - talc which is modified with an amino decane surface. Composition of the Invention The composition of the present invention comprises (a) at least one olefin multi-block heteropolymer; (b) to a fluorene-based olefin-based polymer; and (c) at least one thermoplastic polyamine-based vinegar . In a further embodiment, the functionalized olefinic polymer is present in an amount of less than or equal to 20 weight percent, preferably less than or equal to 15 weight percent, more preferably less than or equal to 1 weight percent of the total weight of the composition. () Weight percent and most preferably less than or equal to 5 weight percent. In another embodiment, the functionalized olefinic polymer is present in an amount of greater than or equal to 5% by weight, preferably greater than or equal to 60% by weight, and more preferably greater than or equal to 7, based on the total weight of the composition. 〇 Weight percentage. In another embodiment, the composition comprises from 75 to 95 weight percent of the total weight of the composition of the olefin multi-block heteropolymer, and preferably from (10) to the weight percent 'its ratio - ethylene / 〇 1__? Block heteropolymer. Preferably, the a-dilute hydrocarbon is a C3_cl〇 a-dilute hydrocarbon, and more preferably is selected from the group consisting of propylene, 1-butene, 1-hexene and octene. In another embodiment, the composition comprises from 1 to 1% by weight of the functionalized olefin-based polymer; and from 99 to 99% by weight of the dilute-smoke multi-segment heteropolymer, which is preferably -ethylene/ (1) thin smoke multi-segment heterogeneous copolymer, hundred 144 200911847 is based on the total weight of the two components. Preferably, the α-olefin is a C3-C1 〇α-olefin' and more preferably is selected a group consisting of free propylene, 1-butene, 1-hexene, and 1-octene. In another embodiment, the composition comprises 7 to 1 weight percent of a 5 functionalized dilute tobacco polymer. And from 0 to 30 weight percent of the olefin multi-block heteropolymer; each weight percentage is based on the total weight of the two components. In another embodiment - the composition comprises 5 to 4 of the total weight of the composition The functionalized olefin-based polymer is preferably from 10 to 35 weight percent, and more preferably from 12 to 30 weight percent. In another embodiment, the composition comprises greater than or equal to the total weight of the composition. 50% by weight of the olefin multi-block heteropolymer, preferably greater than or equal to 55 wt% In another embodiment, a composition of the present invention comprises the composition comprising at least one filler, preferably from 15 to 50 weight percent, based on the total weight of the composition, to 5% by weight, and more preferably Preferably, it is from 10 to 40% by weight. In yet another embodiment, the filler is a citrate. In another embodiment, the filler is a talc. In another embodiment, the filler is a citrate. It is modified with an amino decane surface. In another embodiment, the filler is a talc that is modified with an amino decane surface. 20 In another embodiment, the composition comprises 45 to 60 weight percent The olefin multi-block heteropolymer, preferably from 50 to 55 weight percent; from 5 to 20 weight percent of the functionalized olefin polymer, preferably from 1 to 15 weight percent; and from 25 to 45 weight percent filler, Preferably, it is from 3 Torr to 4 Torr by weight; each weight percentage is based on the total weight of the three components. In yet another 145 200911847 embodiment, the filler is - oxalate. In another embodiment, this The filler is talc. In another embodiment, this group The product comprises 45 to 6 weight percent of a dilute hydrocarbon multi-block heterogeneous total (four), compared with 55 weight percent; from 5 to 5 weight percent of the functionalized dilute hydrocarbon polymer, preferably a weight percent; And 25 to 45 weight percent of the surface modified filler, preferably from 30 to 40 weight percent; each weight percentage is based on the total weight of the three components. In yet another embodiment, the filler is a citrate, It is modified with an amino decane surface. In yet another embodiment, the filler is a talc which is modified with an amine sill surface. One of the compositions of the present invention optionally comprises at least one additive. A slip agent, an anti-caking agent, an anti-AO agent, an anti-mite, and a filler may be added to the composition of the present invention. Basically, one of the compositions of the present invention may comprise at least one stabilizer, such as an antioxidant such as IrganoxTM 1010 and Irgaf® STM ι68 supplied by Ciba Specialty 15 Chemicals. The polymer is treated with at least one stabilizer, substantially prior to extrusion or other melting processes. Other polymer additives include, but are not limited to, ultraviolet light absorbers, antistatic agents, pigments, dyes, nucleating agents, fillers, slip agents, flame retardants, plasticizers, processing aids, lubricants, stabilizers, Smoke suppressant, viscosity control 20, anti-caking agent, release agent, flame retardant, anti-wear and scratch additive, antibacterial agent, antistatic agent and cross-linking agent. In one embodiment, the functionalized flue-cured polymer is present in an amount of less than or equal to 20 weight percent, preferably less than or equal to 15 weight percent of the total weight of the composition, more preferably less than or Equal to 10 weight percent. 146 200911847 In another embodiment, the composition comprises from 15 to 35 weight percent of the thermoplastic polyurethane of the total weight of the composition, and preferably from 20 to 30 weight percent. In another embodiment, the composition comprises from 55 to 80 weight percent of the total weight of the composition of the olefin multi-block heteropolymer, and preferably from 60 to 75 weight percent. The olefin multi-block heteropolymer is preferably an ethylene/(X-olefin heteropolymer. Preferably, the α-olefin is a C3-C10 α-dilute hydrocarbon, and more preferably is selected from the group consisting of propylene, 1 a group consisting of butene, 1-hexene and 1-octene, and preferably 1-octene. 10 In another embodiment, the composition comprises from 55 to 80% by weight of the total weight of the composition. The olefin multi-block heteropolymer is preferably from 60 to 75. by weight. The olefin multi-block heteropolymer is preferably an ethylene/(X-olefin heteropolymer). Preferably, the α-olefin is one. The C3-C10 α-olefin, and more preferably is selected from the group consisting of propylene, 1-butene, 1-hexene and 1-octene, 15 and preferably 1-octyl. In another embodiment The composition comprises from 5 to 10% by weight of the total weight of the functionalized olefin-based polymer; from 15 to 35 weight percent of the thermoplastic polyaminophthalic acid ester; and from 55 to 80% by weight of the olefin multi-block heterogeneous Copolymer. The olefin multi-block heteropolymer is preferably an ethylene/α-olefin 20 hydrocarbon heteropolymer. Preferably, the α-olefin is a C3-C10 α-olefin. More preferably, it is selected from the group consisting of propylene, 1-butene, 1-hexene and 1-octene, and preferably 1-octene. In another embodiment, the composition comprises a composition 5 to 10 weight percent of the functionalized olefin polymer; 20 to 30 weight percent of 147 200911847 thermoplastic polyurethane; and 60 to 75 weight percent of the olefin multi-block heteropolymer. The block heteropolymer is preferably an ethylene/α-olefin heteropolymer. Preferably, the α-dilute hydrocarbon is a C3-C10 α-olefin, and more preferably is selected from the group consisting of propylene and 1-butene. Group 5 consisting of 1-hexene and 1-octene, and preferably 1-octyl. One of the compositions of the present invention may comprise a combination of at least two embodiments as described above. In one embodiment, the invention The composition comprises (a) at least one olefin multi-block heteropolymer; (b) at least one functionalized olefin polymer; and (c) at least one from a thin tobacco polymer and at least one anhydride compound and/or At least one functionalized olefin-based polymer formed from a 10 carboxylic acid compound. In another embodiment, the functionalized dilute hydrocarbon system The polymer is present in an amount of less than or equal to 20% by weight based on the total weight of the composition, preferably less than or equal to 15% by weight, more preferably less than or equal to 10% by weight, and most preferably less than or equal to 5 weight percent. In a preferred embodiment, 15 the functionalized olefin polymer is present in an amount of less than or equal to 10 weight percent of the total weight of the composition, and preferably less than or equal to 5 weight percent. In another embodiment, the composition comprises from 10 to 90 weight percent of the total weight of the thermoplastic polyurethane urethane, preferably as hereinbefore described, and from 90 to 10 weight percent of at least the olefin multi-block heteropolymer. Things. In still another embodiment of the invention, the composition comprises from 1 to 10 parts by weight of the functionalized olefin-based polymer. In another embodiment, the composition comprises from 10 to 50 weight percent of the total weight of the composition of the thermoplastic polyaminophthalic acid vinegar, preferably from 25 to 40 weight percent, and more preferably from 25 to 37 weight percent. Preferably, it is as described above. In another embodiment, in another embodiment, the composition comprises from 55 to 80 weight percent of the total weight of the group 148 200911847, the olefin multi-block heteropolymer, and preferably 60 to 75 weights are eighty-eight knives ratio, and more preferably from 63 to 75 weight percent. In another embodiment, t z this composition comprises 55 to 80 5 of the total weight of the composition

The hexagram is more preferably from 60 to 75 weight percent, and more preferably from 63 to 75 weight percent, more preferably as described above. Preferably, the olefin multi-embedded heterogeneous copolymer is an ethylene multi-block heteropolymer. Preferably, the two are selected from the group consisting of propylene, 1-butene, 1-hexene and !-octene. a group, and preferably "dilute. In an embodiment, in the case of a known embodiment, the composition comprises a functional weight of from 1 to 10 weight percent eight θ S in the total weight of the composition. An olefin-based polymer; from 15 to 50 parts by weight of the thermoplastic polyamino group (IV), preferably as described above and having a percentage by weight of 55 to 80 parts by weight of the smoke multi-block heterogeneous copolymer. Preferably The smoke multi-block heteropolymer is a _B (tetra) block heteropolymer. Preferably, the α olefin is selected from the group consisting of propylene, butadiene, hexene and octene, and is preferably 1-octene.

In another embodiment, the composition comprises from 0 to 10 weight percent of the functionalized olefinic polymer of the total weight of the composition; from 25 to 4 weight percent of the thermoplastic polyurethane, preferably It is as described above, and is composed of 60 to 75 weight percent of the olefin multi-block heteropolymer. Preferably, the _ 2 〇 multi-block heteropolymer is an ethylene multi-block heteropolymer. Preferably, the α-dilute hydrocarbon is selected from the group consisting of propylene, r butene, and κ hexene. · A group of Xinchengcheng, and preferably 1-inch. In one embodiment, the composition comprises from 10 to 50 weight percent of the functionalized ethylenic polymer of the total weight of the composition; from 15 to 50 weight percent 149 200911847 to thermoplastic polyurethane vinegar, Preferably, as described above, and from 55 to 80% by weight of the ethylene multi-block heteropolymer, it is preferably as described above. Preferably, the α-olefin is selected from the group consisting of propylene, 1-butene, 1-hexene and 1-octene, and is preferably 1-octene. In another embodiment, the composition comprises from 1 to 10% by weight of the functionalized dilute hydrocarbon polymer based on the total weight of the composition; from 25 to 40% by weight of the thermoplastic polyurethane, preferably As described above, and from 60 to 75 weight percent of the ethylene multi-block heteropolymer, it is preferably as described above. Preferably, the α-olefin is a group selected from the group consisting of propylene, 1-butene, 1-hexene and 1-octene 10, and is preferably 1-octene. In another embodiment, the olefin multi-block heteropolymer is present in an amount greater than or equal to 50 weight percent and the amount of polyurethane is less than or equal to 50 weight percent, the percentage of which is greater than the olefin The combined weight of the block heteropolymer and the polyurethane vinegar. Preferably, the amount is from 50 weight percent to 15 weight percent of the olefin multi-block heteropolymer, from 45 weight percent to 10 weight percent of the thermoplastic polyurethane, and more preferably from 55 to 85 weight percent. A percentage of the olefin multi-block heteropolymer, and from 45 to 15 weight percent of the thermoplastic polyurethane. In another embodiment, the composition comprises from 55 to 80 weight percent of the olefin multi-block heteropolymer, and from 20 to 45 weight percent of the polyurethane. The amount selected is a total of 100 weight percent. All individual values and sub-ranges from 50 to 90 weight percent of the olefin multi-block heteropolymer are included and disclosed in this specification. All individual values and sub-ranges from 50 to 10 weight percent of the polyurethane are included and disclosed in this specification. Preferably, the olefin multi-block heterogeneous 150 200911847 copolymer is an ethylene-rich multi-block heteropolymer' and the alpha-dilute hydrocarbon is selected from the group consisting of propylene, 1-butene, hexene and 1-octene. The group, and preferably 1-xin. In another embodiment, 'the composition of the present invention comprises 50% by weight or more of an olefin multi-block heteropolymer' and preferably 60% by weight of 5 or more dilute hydrocarbon multi-block heteropolymer, and 50% by weight or less of the olefin multi-block heteropolymer and preferably 40% by weight or less of the thermoplastic polyaminophthalate. In one embodiment, the composition comprises from 5% by weight to 80% by weight of the olefin multi-block heteropolymer, and

10 15

20 is preferably from 55% by weight to 77% by weight of the olefin multi-segment heteropolymer; and from 20% by weight to 50% by weight of the thermoplastic polyamino phthalic acid, and preferably from 23 to 45% by weight Thermoplastic polyurethane; the percentage of both is the combined weight of the olefin multi-block heteropolymer and the polyurethane. Preferably, the olefin multi-block heteropolymer is a poly(ethylene) olefinic copolymer, and the (X-ene is selected from the group consisting of propylene, butene, 1-hexene and 1-octene. a group, and preferably 丨-octene. In another embodiment, the composition of the present invention comprises greater than 85 weight percent of the composition of the total weight of the composition of the nucleus and the thermoplastic polyamine The combined weight of the acid ester is preferably greater than 9% by weight, and more preferably greater than 95% by weight. Preferably, the olefinic multi-stage polymer is a heteropolyethylene copolymer of ethylene. The olefin is selected from the group consisting of = ruthenium, 1-butadiene, 1-hexene, and 1-octene, and is preferably r-sin. If the composition for carrying out the present invention contains a polymerization different from the foregoing The components of the component, such as fillers, pigments, etc., comprise a total weight of the blend of more than 85 wt%, difficult to be 9 g by weight, and more preferably greater than 151 200911847 95 wt% of the olefin multi-block heteropolymer a combination of a thermoplastic polyurethane and a functionalized olefin polymer. In one embodiment, 'for this The composition of the present invention has a melt index (12) of from 0.01 to 100 g/min, preferably (U to 5 〇g / 1 〇 min, 5 and more preferably from 1 to 40 g / ΙΟ min, And preferably from 5 to 40 g/l〇, as measured using ASTM D-1238 (190 ° C, 2.16 kg load). In another embodiment, the composition has a greater than or equal to 〇.〇1 g I2 of /i〇 minutes, preferably greater than or equal to 1 and more preferably greater than or equal to 5 g/10 minutes. In a further embodiment, the composition has a less than or equal to 1 〇〇g/l 〇 I2 of 10 minutes, preferably less than or equal to 50 g/10 minutes and more preferably less than or equal to 20 g/ΙΟ minutes. The composition ι2 is measured as a pure blend, that is, nothing else can be significant A blend that affects the 12 measured component. In another embodiment, the composition has a percent crystallinity of less than or equal to 5 percent, preferably less than or equal to 3 percent and more preferably less than 5 percent. Or at a percentage, as measured by DSC. In one embodiment, such polymers may have a percent crystallinity of from 2 to 50 percent, including from 2 to 50 percent There are values and sub-ranges. The crystallinity of this composition is measured as a pure blend, that is, a blend of other components that can significantly affect the measurement of crystallinity. 20 In another embodiment, the composition is greater than Or a density equal to 0.855 g/cm3 (or g/cc), preferably greater than or equal to 〇86 g/cm3 and more preferably greater than or equal to 0.87 g/cm3. In another embodiment, the composition has a The density of less than or equal to 1 g/cm3, preferably less than or equal to 〇97 g/cm3, more preferably less than or equal to 0.96 g/cm3, and most preferably less than or equal to 〇95 g/cm3. 152 200911847 In one embodiment, the density is from 0.855 to 0.97 g/cm3, preferably from 〇86 to 0.95 g/cm3, and more preferably from 0.865 to 0.93 g/cm3. This composition density is measured as a pure blend, i.e., a blend of other components that can significantly affect density measurements. In such embodiments, wherein the composition comprises up to 5 less fillers, for example, barium sulfate, talc, etc., the maximum density of which does not exceed jg/cm3, for example, the maximum density may depend, for example, on the nature and amount of the filler. 1.4 g/cm3. In another embodiment, the composition is pure and in a manufactured form having a tensile strength of 5 to 40 MPa (MegaPascal), preferably 8 to 3 Torr 10 MPa and more preferably 9 to 20 MPa. In another embodiment 'this composition is pure and in a manufactured form having a length in the direction of the mechanism or transverse mechanism having a length of 50 to 60010 minutes as measured by ASTM D-638-03, or from 50 to 50010 minutes. In another embodiment, the composition has a melt strength of 〇 5 to 5 〇 15 cN (centiNewton) in a pure form, and preferably from 〇·5 to 2〇 cN and more preferably from 0.5 to 10 cN. In another embodiment, the composition is in a pure form at room temperature or 23. 〇 has a surface tension of 10 to 100 dyn/cm, and preferably 2 〇 to 7 〇 dyn/cm ' and more preferably 30 to 50 dyn/cm.

In another embodiment, the composition has a surface tension of greater than or equal to 32 dyn/cm, more preferably greater than or equal to 33 dyn/cm, and most preferably greater than or equal to 32 dyn/cm at room temperature or 23 ° C in a pure form. Equal to 35 dyn/cm. In another embodiment, one of the compositions of the present invention, when at a temperature of 2 〇〇乞 die (180 ° C - 190 ° C region temperature) at 80 lbs / hr through a thickness of 40 mils and 2 153 200911847 inches width In the case of a flat hanger die extrusion, a surface energy > 35 dyne/cm ° can be produced. In another embodiment, the composition of the present invention is formed into a dust-extruding sheet which is aged at 120 ° C for 500 hours (ASTMD_882) The initial elongation of at least 5 50 percent is maintained after _ 〇 2), preferably at least 60 percent. In another embodiment, the present invention provides a composition as hereinbefore described, and wherein the olefin multi-block heteropolymer is present in a continuous or co-continuous phase with the thermoplastic polyurethane, and the olefin multi-block heterogeneous The copolymer is preferably an ethylene/α-olefin multi-block heteropolymer. In another embodiment, the present invention provides the composition as described above, and wherein the olefin multi-block heteropolymer is present in a co-continuous phase with the thermoplastic polyurethane, and the olefin multi-block heteropolymer Preferred are ethylene/α-olefin multi-block heteropolymers. The composition of the present invention can be prepared by combining at least one of a plurality of heterogeneous heteropolymers 15 and at least one thermoplastic polyurethane, and the olefin multi-block heteropolymer is preferably at least one ethylene/α_ Olefin multi-block heteropolymer. Basically, the composition of the present invention is prepared by blending a polymer component (olefin multi-block heteropolymer, polyamino phthalate, and functionalized olefin polymer) in a post-reactor. The post-reactor blending description is an extrusion in which two solid polymers are fed into the extruder and substantially mixed into a substantially homogeneous composition. The composition of the present invention can be crosslinked and/or foamed. In a preferred embodiment, the composition of the present invention can be prepared by blending components in a melt process. In yet another embodiment, the melting process is a melt extrusion process and is preferably an "on-line" composite process. 154 200911847 In another embodiment, the composition further comprises a polypropylene polymer component such as a propylene homopolymer, a copolymer of propylene and ethylene or at least _α-smoke, or a homopolymer. A blend of copolymers, a nucleating homopolymer, a nucleating copolymer, or a nucleating blend of a homopolymer and a copolymer. The α-olefin in the propylene copolymer may be 1-butene, 1-pentene, 1-hexene, b-glythene, octanoic or 4-mercapto-1-pentene. Ethylene is a preferred comonomer. The copolymer may be a random copolymer or a copolymer of a segment or a copolymer of a random copolymer and a copolymer of the segment. This polymer can also be branched. Thus, the component is preferably selected from the group consisting of a polypropylene homopolymer and a propylene/ethylene copolymer or a mixture thereof. The component may have a melt flow rate (MFR) of from 0.1 g/10 min to 150 g/1 min (230 t: and 2.16 kg weight), preferably from 0.3 g/l min to 60 g/min, more Preferably, it is 8 g / 1 〇 minutes to 4 〇 g / 1 〇 minutes, and the best is 0.8 g / ΙΟ minutes to 25 g / l 〇 minutes. All individual values and sub-ranges of (% to (1) minutes are included and disclosed in the present invention. The group also has a density of from 0.84 g/cc to 〇92 g/cc, preferably from 〇85 to 0.91 g/cc, and more preferably from about 86 g/cc to about 9 g/cc. . All individual values and sub-ranges from 叭 84 to 0.92 g/cC are included and disclosed in the present invention. This component can have greater than 125. (: Melting point. As used herein, '"nucleation" means that a polymer can be modified by the addition of a nucleating agent such as Millac®, which is commercially available from Milliken Corporation as a sorbitol. Other conventional nucleating agents may be used. Additives such as treatment oil, hydrazine, anti-caking agent, anti-AQ agent, anti-UV agent, and filler may be added to any of the compositions. Basically, the product may have at least one stabilizer. Such as antioxidants such as c such as 155 200911847

Specialty Chemicals' IrganoxTM 1010 and IrgafosTM 168. An example of an antioxidant is the Irganox® 1076 inhibitor available from Ciba-Geigy Corp. The polymer is treated with at least one stabilizer, substantially prior to extrusion or other melting processes. Other polymer additives include 5 but not limited to UV absorbers, antistatic agents, pigments, dyes, nucleating agents, fillers, slip agents, flame retardants, plasticizers, processing aids, lubricants, stabilizers , smoke inhibitors and agglomerates. The remaining additives include, but are not limited to, surface tension modifiers, colorants, treatment oils, waxes, foaming agents, anti-caking agents, foaming agents, antistatic agents, release agents, flame retardants, anti-wear 10 And scratch additives, antibacterial agents, antistatic agents and crosslinkers. One of the compositions of the present invention may comprise a combination of embodiments suitable for at least two of the foregoing. Application 15 20 The composition of two or more components of the heart or at least three components can be used in more than four different applications. For example, the invention provides an article comprising at least one component formed from a composition of the invention, the composition being as described herein. The composition of the present invention is particularly suitable for injection molding articles, blown film articles, pressure objects, extruded sheets 'bonding' and bonding sound between extruded sheets, bonding layers between two mold sheets, and between films The joint layer and the type of outer door are connected with 3 layers, fibers, and dispersion (water 3 blanket component; artificial leather; human (9) 5). Other items include ground, awning, adhesive, fabric, wire, slightly, Wei, (10), coating, ^f piece, foam laminate, shoe last, laminate, general plastic shoes (for example! ^子&shoe bottom and outsole; such as shoes and rubber footwear or synthetic and natural leather 156 200911847 leather objects; or automotive products (such as airbags, headrests, armrests, carpet mats, coatable cars) Components, etc., and adhesive to KEVLAR. In another embodiment, the article is an automotive outer layer such as an instrument panel skin or door panel outer layer, awning, waterproof garment, roof structure (eg, for 5 roof applications) Such as insulation bonding, liquid roofing, building sealant, expansion joints, wet room sealant, asphalt roof, acrylic resin bonded roof, asphalt joint, PUR-adhesive reforming epoxy resin, amine Binder for urethane or propylene based substrate; steering wheel; powder coating; powder filling molding; consumer product; grip; handle; computer component; belt; 1 flower; shoe assembly; Conveyor belt or timing belt; lubricating oil and Oil component; fiber; film; film coverings of different sizes; fabric; artificial leather; injection molded articles, such as injection molded and / or coated toys; artificial turf; artificial leather; Kevlar adhesive; Film coatings of different sizes; dispersions; powder coatings, powder grout molding or spin casting molding (basically, each having 15 particle sizes of less than 95 μm), durable consumer goods, grips, handles, computer groups a (for example, a key 塾), a belt, a fabric/polyurethane vinegar (IV) adhesive for an envelope/envelope laminate (eg, decals and footwear), for example, in combination with a layer of abrasive to an extruded article, Transmits timely belts, fabrics, carpets, artificial turf coatings, wires and cables, and raincoats with similar protective clothing 20 (hot melt or other). X special applications include adhesives for polyurethane film and foam, adhesives for bismuth, Japanese, dyes, coating adhesives and coating adhesives; splicable applications; automotive interiors and exteriors a compatibilizer for the polymer composition; and a fluxing agent for the polymer composition. 157 200911847 In particular, the compositions of the present invention can be used in the following applications: (a) outer soles, mid soles, outsole and reinforcements assembled in standard polyurethane bonding systems currently used in the footwear industry, (b) Applied with a sole and mid sole for polyurethane coatings, currently used in footwear, and (c) multi-layer soles and midsole 5 polyolefin and two-component polyamine phthalate overpressure molds . In addition, the compositions of the present invention can be used in other applications, such as automotive applications and structural applications. Automotive applications include, but are not limited to, the manufacture of shock absorber dashboards, straight panels, soft rafts, interior trim and outer layers. Structural applications include, but are not limited to, the manufacture of furniture and toys. 1〇 Other applications include coextruded film bonding in which at least one substrate is compatible or reactive with functional groups such as hydroxyl groups, and layering of polyolefin film to other polar substrates (e.g., glass layer cooperation). Further applications include artificial leathers adhered to polar substrates such as polyurethanes, polyethylenes (PVC) and others. Artificial leather is used for car interiors that are bonded to polyurethanes, and 15 for seat and headliners. The compositions of the present invention are also suitable for use in sanitary products such as rags, cleansing tissues, foams or directly dyeable fibers. The composition of the present invention promotes the hydrophilicity of an elastomer for a novel membrane structure of separation or gas permeability. The composition of the present invention is also applicable to a 20 self-adhesive elastomer as a metal or fabric structure for automobiles. As stated above, the compositions of the present invention are also suitable for use in blends and compatibilizers which promote interaction with polar polymers, such as TPU, EVA, PVC, PC, PET, PLA (poly-ILS Chu), poly Amine vinegar and PBT. This composition is useful as a novel compound for use in footwear, automobiles, consumer durables, and appliances, electronics housings, clothing, and conveyor belts. 158 200911847 The composition of the present invention can also be used as a compatibilizer between natural fibers and other polyolefins for applications such as wood bonding formulations or cellulose bonding formulations. The compositions of the present invention can also be used in admixture with at least a polyether block guanamine such as Pebax® polymer available from Arkema. The composition of the present invention may also be used as a heterogeneous impact modifier. Further, the amine group of the composition of the present invention may be protonated or alkylated to form a quaternary derivative or isomer for use as an anti-. The compositions of the present invention can also be used to promote interaction with fillers, such as emulsified stone, carbon black or clay, for use in the formulation of toners, tires, and other coating compounds. The composition of the present invention can also be used for engine oil viscosity modification H) agent, engine oil dispersant, dyeable or printable fiber for clothing, paint adhesion promoter, glass adhesive, metal guess (10) and agent, dispersion, The composition of the primer and the polymerization agent. Viscosity 5 Accordingly, the present invention also provides a coating substrate formed from the present invention-constitution as described herein, and comprising at least 15 polymers, alkyd resins, cellulosic materials, melamine resins, Linalic acid vinegar resin, amino carboxylic acid vinegar resin, poly-lipid, ethylene diacetate, polyol and alcohol. In yet another embodiment, the coating is two = 枓. In another embodiment, the coating is an organic solvent based coating. The embodiments of the present invention are applied to a wide range of coating formulations. The main components of the materials and coatings are solvents, binders, pigments, and coatings. The combination of binders and solvents is considered as coating carrier 7 And additive dispersion"". The amount of each constituent varies in a particular coating' but the solvent traditionally reaches the secret percentage of the total formulation. The solvent includes toluene, dimethyl benzene, methyl ethyl hydrazine, methyl isobutyl amide; 159 200911847 = mixture usage amount (10) weight percent, color = fine weight percentage. Used in coatings II:: Materials include: acryl-based polymer, alkyd resin-cellulose t 5 10 15 20 resin, poly π = , melamine resin, amine group, polyol B (tetra) resin, urethane Vinegar wax, ,, heat machine materials such as titanium dioxide (rutile), mica flakes, iron, gas cut, lack of and the like. The film and the gas material are provided by a coating material, which is formed by a polar substrate and a coating of the present invention. - Through-spraying, the present invention provides a super-mode (four) piece formed from a substrate formed by the present invention and comprising a polar material ::::::. In still another embodiment, the article is a grip, a compact (four) towel, and the present invention provides a super-mode small one comprising a multi-purpose, such as a base sheet having a different thickness, and preferably having To (four) ί. The surface of the fabric which is bonded to the moon and formed is substantially formed by pressing at a temperature of 140 C. This object has good adhesion. This material can be bonded to the exposed surface of the film of the composition of the present invention by using conventional _ technology and laminating with a hydrocarbon such as pressure and heat, s, a second polycarbonate having a surface of the mash. . - The present invention also provides a laminate structure comprising a first layer formed from a composition of the invention as described herein and a second layer formed from a composition of 3 polar materials. In yet another embodiment, the layers are in the form of a foam. In another implementation, these layers are in the form of fabrics 160 200911847. In yet another embodiment, the laminate structure is in the form of an awning, waterproof garment or car skin or steering wheel. In another embodiment, the present invention provides a laminate structure comprising polycarbonate as a base sheet having different thicknesses, and preferably having at least 5 fabric surfaces to allow adhesion of one of the compositions of the present invention Above, it is basically made by a compression molding process at 14 (TC medium temperature. This laminate shows excellent adhesion; for example, a polyolefin functionalized with a secondary amine group at a concentration of 1.1 weight percent The peel strength is 1 N/mm. The article can be further laminated with a polyolefin using conventional splicing techniques, such as by pressure and heat. In addition, a second polycarbonate sheet having a fabric surface can be laminated. In the composition of the present invention (having a fabric surface at the interface), another embodiment of the present invention is a multilayer structure of a polycarbonate and a polyolefin film 'this arrangement to increase the toughness of the final structure. Another embodiment is The present invention is an elastomeric coating deposited on the surface of a polycarbonate which provides a coating of a scratch resistant component which is readily formed by heat, for example at a temperature of about 16 〇t: temperature. Also provides one The first component and the second component of the molding x fraction are formed of a polar material, and the second component is formed of a composition of the invention as described in the above. - In the embodiment, this part is in the form of a π car outer layer, a decal, a shoe, a conveyor belt, a timing belt or a durable consumer product. "Laminate,,, "β person, LL B layer cooperation" and the like The word means that at least two layers are closely joined to each other right--.. for example, a film layer. The laminate comprises a tantalum article carrying a coating. The layer a is not a blend, although one of the laminates Or more than one 161 200911847 layer may comprise a pusher. ''Polarity', 'Polar polymer' and its similar words mean that the polymer molecule has a permanent dipole, ie the polymer molecule has a positive end and a The negative end. In other words, the electrons in the polar molecule are not equally divided into 5 in the molecular atom. Conversely, "non-polar,", "non-polar polymer," and the like mean that the polymer molecule does not have a Permanent dipole, that is, the polymer molecule does not have a positive end and a negative end. The electrons in the molecule are substantially equally distributed in the molecular atom. Most hydrocarbon liquids and hydrocarbon polymers are non-polar. The polymers substituted with carboxyl groups, hydroxyl groups and the like are usually polar 10 polymers. The resulting article has a relatively low surface energy, i.e., less than about 32 dyne/cm, and the article made from the polar polymer has a relative surface energy, i.e., 32 dyne/cm or more. The non-polarity of the present invention. The material substantially comprises at least one non-polar thermoplastic olefin polymer, substantially an elastomer, without any significant amount of polar functional groups, such as hydroxyl groups, 15 carboxyl groups, carbonyl groups, esters, ethers, decylamines, thiols, halides, and The polar material of the present invention basically comprises at least one polymer containing one or more polar s b groups. The polymer package typically comprising at least a polar functional group is not limited to polyester, polyether, poly Lactic acid, polycarbonate, nylon, multi-polymer, polylith, polyurethane, polyvinyl alcohol, poly(vinyl acetate), 20 poly (chlorinated ethyl), acrylonitrile, ABS, poly Amidoxime esters, and polyoxyalkylene oxides. A polar functional group, and the like, means that a polymer does not contain a ~~., a member of a polar functional group to impart at least about 32 dyne/cm to an article made therefrom. Surface energy. "Over-pressure" and its similar words are a process in which a resin is injected - containing 162 200911847 in a model with a preset substrate, and molded on the substrate. The overmolding is basically made by making the resin super difficult Used to modify the sex month b and properties of the final product on _ other polymers. Overmolding can be used to form seamless, integrally molded components. Overmoulding components include 5 pullable grips on power tools and kitchen appliances. The handle, which provides additional grip properties without the attendant hygiene problems associated with the mechanical component. The substrate can be any suitable material, such as a plastic, metal or ceramic component. "Molded coating" and similar words are Refers to an article containing at least two components (an injection molding component and a substrate) that are joined together. The injection molding component is placed on the top of the substrate and exits the outside of the molding die. An adhesive can be used to bond the molded article to Substrate. The substrate can be any suitable material, such as a plastic, metal or ceramic component. The substrate to which the composition of the present invention can be applied includes a variety of materials, including polar and non-polar, such as It is not limited to a composite of a polymer, a metal, a wood, a cement, 15 glass, a ceramic, and two or more such materials. Alternatively, such materials may be applied to an article formed of the composition of the present invention containing the same. Methods of application include coating, printing, dyeing, overmolding, and the like, and including variations of each such as painting, spraying, dipping, sowing, and other methods. The compositions of the present invention may be applied prior to application, Crosslinking to the substrate between or after, and it may be crosslinked in any convenient manner, for example, peroxide, sulfur, moisture, calcination, II shot, heat, and the like. In one embodiment The composition of the invention is applied to a substrate, and the composition of the invention is crosslinked at the time of application and/or after application. For crosslinking, the composition of the invention typically contains unsaturation, for example, a diene-containing PO. 163 200911847 In the case of the invention, the composition of the invention may be in the form of a layer, in particular between a polar and a non-polar polymeric material = a layer of __ and a polar polymer such as polylactic acid or polyamine or (iv) film, the non-polar Film layer such as polyethylene = Dilute. The inventive composition of the invention is particularly suitable for the surface bonding of polyethylene or polypropylene of a hetero- or a molded article to (8)-ethylene/acrylic acid copolymer (EAA) or PLA or poly-W pair Benzene _ (4) Take the surface of the polymer or the molded object. It can be combined with co-extrusion 10 pressure, extrusion layer cooperation, adhesive layer cooperation, and / or foam secret or extrusion to produce Such a laminated structure includes a structure in which the layer contains a foam.

The composition of the present invention can also be used in a dispersion, such as an aqueous dispersion for a primer of a dilute hydrocarbon footwear to promote adhesion of a polyurethane coating (adhesive fine T, _, PP, ^P =;; M 15 or other non-polar elastomers are rich in elastomeric τρ〇 or combinations thereof, etc.). In general, the compositions of the present invention are useful in bonding applications such as overmolding applications, coatability and printability. This composition can also be used in dye applications. Special bonding applications include adhesives for polyurethane vinegar in the automotive industry, such as the outer layer of the instrument panel and the outer layer of the door panel, adhesives for footwear applications, 20 such as various footwear components and Adhesive for vinegar in EPDM conveyor belt. The aqueous dispersion prepared by the composition of the present invention can be used as a binder in footwear to adhere the polyolefin and polyaminophthalate layers. The aqueous dispersion based on the composition of the present invention can also be used as a primer for an olefin footwear component to promote the adhesion of the polyurethane adhesive to the adhesion of the leather. Other applications include fabric-coated adhesives (bonded to PET, nylon, PP, TPO containing PEE, EPDM or other non-polar elastomers rich in elastomers, or combinations thereof, etc.). The composition of the present invention can also be used as a coating, coating, adhesive, adhesive, film, printable surface, dyeable film and fiber, artificial leather, protective cloth, human turf, 5 carpet fiber, fabric, medicine A set of articles (eg, blood bags and tubes), toys, flexible overmolded articles, soft grips, sportswear, and the like or any application intended to be bonded to a polyolefin. Others apply to the description in this article. Other particularly preferred applications include automotive thermoformed outer layers, PU foam adhesives (preferably aqueous primers that do not use the current chlorinated maleate-based 10 smoke), and household packaging materials - Requires high moisture penetration (100% PELLETHANEtm 2i〇3_7〇a meets requirements) and good adhesion to polypropylene fabrics (cotton yarn); adhesive film (blown or cast film); coextruded film, which uses POE /TPU is a thin adhesive bonding layer (for example, a roofing film that requires PU glue bonding). In such cases, the compositions of the present invention are typically employed with diols, isocyanato, OE and/or compatibilizers. The compositions of the present invention can result in an increase in surface energy (> 37 dyne/cm) for bonding to polar materials. If the TPU is fully aliphatic (no aromatic, no unsaturation) - POE/TPU system can be used as a weather resistant coating (as opposed to an adhesive bonding layer). In one embodiment, the invention provides a method for imparting high frequency (HF) fusion properties and/or printability to an article comprising a low surface energy material, i.e., a non-polar material eHF_welding. Polyolefin sheets or films may be permitted for applications such as roofing films, stationery, artificial leather, etc., where polyolefins are contemplated for use due to cost/performance advantages and recyclability. Materials and procedures for HF_fusion properties are known in the art and are generally described in 165 2009 Π 847 US 2004/m7791. Known methods include the addition of a smectite or a resin containing a polar functional group such as a Li-graft resin, or EAA, EEA, EMA, or EMM polymer to - before the non-polar polymer is melted or printed. Non-polar hydrocarbon resin. However, such methods provide poor (10) connectivity and/or printable results with respect to (4) the desired (four) amount and under phase (iv) conditions in accordance with embodiments of the present invention. In another embodiment, the invention provides a method of imparting coatability, printable H, dyeability, and overmolding to an article comprising a low surface energy material. - This embodiment of the invention works well with a wide range of coating formulations. ♦ The main components of marine coatings and coatings are solvents, binders, pigments and additives. In the coatings, the combination of binder and solvent is considered as the coating carrier. The pigments and additives are dispersed in a carrier. The amount of each component varies depending on the particular coating, but the solvent has traditionally reached about 60% of the total formulation. Typical solvents include 2 toluene, hydrazine, methyl ethyl ketone, methyl isobutyl ketone and water. The combination ^ accounts for about 3 〇 Wt%, the pigment accounts for 7 to 8 wt% and the additive is 2 to 3 wt%. Some of the polymers and other additives that can be included in the coating formulation include: propylene-based poly-, alcohol-ester, cellulosic materials such as cellulose acetate butyric acid, triacetin, and amino phthalate Resin, polyester resin, ethyl acetate vinegar 20 tree sorghum, urethane carboxylic acid resin, polyol, alcohol, inorganic materials such as rutile ruthenium dioxide, mica flakes, iron oxide, oxygen cut, Ming and similar . By way of non-limiting example, the compositions of the present invention can be used to promote the following viscous σ (i) PU-thermosetting foams and polyolefin elastomers (p〇E), particularly in extruded sheets, crucibles or Interfacial bonding layer, (ii) POE/pd-TPU blowing; 166 200911847 (iv) Pure TPU and P〇E, (iv) T: olefin rubber and τρυ or - thermoplastic sulfide (TPV) as described in EP 0 468 947; (v) in the extrusion or molding process of the polyester or other polar plastics and cross-linking gasification (v deleted and TM fibers, such as carpets, artificial turf, etc. 5 fillers and non-polar materials, such as Wire and electric gauge insulators, coatings, etc.: (iv) hot melt bonding difficult-to-polar substrates; (iv) pGE and pdTpu objects, such as footwear and automotive parts; and (x) aqueous dispersions, which can produce a variety of articles, such as films. The substrate to which the composition of the present invention can be applied includes a wide range of materials, including polar and non-polar, such as but not limited to polymers, metals, wood mud, glass, and a variety of materials from at least two of these materials. Alternatively, such materials may be applied to the article containing the blend. The application method includes coating. , printing, dyeing, overmolding and the like, and including variations of each of the above, such as coating, spraying, dipping, extrusion, etc. The composition of the present invention can be applied prior to application to the substrate. Crosslinking during and after, and it can be crosslinked by any conventional method, such as peroxides 'sulfur, moisture, Wei, Han, heat, and the like. In one embodiment, the composition is applied to a base. The composition, and thus, the composition is crosslinked when applied and/or after application. For crosslinking, the compositions of the present invention typically contain unsaturation, for example, a dilute p〇 and/or a non-20 hydrogenated TPU. In one embodiment, the composition of the present invention acts as a bonding layer between polar and non-polar materials, particularly between polar and non-polar polymeric materials, for example, in a film layer such as polyethylene or polypropylene. With a polar polymer film layer such as t-lactic acid (PLA) or polyamine or polyester. The pd_Tpu of the present invention is particularly suitable for 167 200911847 as a surface for polyethylene or polypropylene film or a molded object bonded to B Dilute/acrylic acid copolymer (EAA) or PLA or polyethylene terephthalate ρΕτ) A film or surface bonding layer of a molded article. Any process that can be combined with a total of 5 extrusion, extrusion layering, adhesion layer cooperation, and/or foaming 5 extrusion can be used. To produce such a laminate structure, including a structure in which a foam is contained. In another embodiment of the present invention, there is provided an article comprising a film formed from a composition of the present invention and a polyurethane film. a foam, and wherein the film is bonded to the surface of the polyurethane foam. This article may be a meter. In yet another embodiment, the film of the present invention and the polyurethane are used. The bond between the ester foams is stronger than the bond between the foam and the other films, and the other films comprise the same composition of the film of the present invention except for the functionalized polyethylene. In an embodiment of the invention, a film formed from the composition of the invention is provided. In another embodiment, a film comprising at least two layers is provided, and at least one of the layers 15 is formed from a composition of the invention as described herein. In another aspect of the invention, the film is formed by co-extrusion or layer cooperation. The film may contain at least one of the character characteristics as described herein, and preferably comprises a co-continuous phase of the ethylene-based polymer and the polyurethane. Articles containing at least a component, containing the film, or formed therefrom are also provided. The article package 20 includes, but is not limited to, automotive interior components, instrument panel outer layers, fabric coatings, vacuum forming outer panels, footwear component layers & sheets of other articles. This article can be prepared by the various methods discussed herein. In another embodiment of the invention, a film is provided comprising at least three layers, and at least one of which is formed from a composition of the invention as described herein. In another aspect of the invention of 168 200911847, the film is formed by co-extrusion or layer cooperation. The film may contain at least - a character as described herein, and preferably comprises a co-continuous phase of the ethylene polymer and the polyurethane. Articles containing at least a component, containing such a film, or formed by such a film are also provided. This item - 5 pieces including but not limited to automotive interior components, instrument panel outer layer, fabric coating, • hollowed out profile, footwear components, laminated sheets and other items. This item can be prepared by the various methods discussed herein. In another embodiment, the present invention provides a film comprising at least two layers, and wherein at least one layer is formed from the composition of the present invention, and wherein at least the other H) layer is comprised of -B having a brightness intensity greater than or equal to 5 cN The composition of the dilute/ingholic heteropolymer is formed. The invention further provides an article comprising the film or the article. The invention also provides articles comprising at least one component formed from the compositions of the invention described herein. The article can be prepared by at least a separate operation, 15 including but not limited to extrusion, thermoforming, blown film, injection molding, foaming; & calendering process. In the embodiment - the articles described herein are non-automotive items and can be used in non-automotive applications. The invention also provides methods of making the compositions and articles described herein. The invention is susceptible to various embodiments of the compositions, articles and methods described herein, and combinations of at least two embodiments. DEFINITIONS Any numerical range set forth herein includes all values in one unit increments from the lowest value to the highest value. 假 任何 Any any amount of any lower value between any higher value of at least two units. For example, if the description - composition, physical or 169 200911847 mechanical properties, such as molecular weight, viscosity, melt index, etc., from 100 to 1,000, all individual values such as 100, ΗΠ, 1 () 2, etc., and sub-range such as 1 〇〇 to 144, 155 to 170, 197 to 200, etc. are apparently listed in the present specification. For a range of 5 10 15 20 containing a value less than 1 or containing a number greater than the k component (for example, Μ, 1.5, etc.), the unit is considered to be "face, care, 〇 1 or 〇". For a range containing less than 10 (e.g., (1)), one unit is substantially regarded as 〇·1. All of the possible combinations of numerical values listed between the lowest value and the highest value are considered to be expressly described in this specification. As discussed herein, the numerical ranges recited are with respect to melt index, flow rate of the melt, molecular enthalpy distribution, percent crystallinity, density, and other properties. θ herein is a composition, a material comprising a material composition containing the composition, and a reaction product and a decomposition product formed from the material of the composition. The term "substance" means a blend of at least a compound. This blend may or may not be miscible (not phase separated at the molecular level). This blend may or may not be phase separated. The % may or may not have at least one major configuration as determined by penetrating electron maps, light scattering, X-ray scattering, and other methods known in the art. The term "polymer," as used herein, refers to a polymeric compound prepared by polymerization of a polymeric monomer, whether the same or different. The generic name 2 is thus meant to include "homopolymer," I, which is generally used to refer to a polymer prepared from a styrofoam type monomer, and "a heterogeneous copolymer, defined as a post-product and a propylene/α-olefin polymer," is hereinafter described as a description of Zha Ming. Heterologous copolymers. QC 170 200911847 As used herein, "heteromeric copolymer" 1 refers to a polymer prepared by polymerization of at least two different forms. The generic term heteropolymer thus includes "copolymer," It is used to refer to polymers prepared from two different types of monomers, and polymers made from at least two different types of monomers. As used herein, "olefin-based polymer," means a polymeric olefin monomer comprising at least 50 mole percent, such as ethylene or propylene (based on the total amount of polymerizable monomers)' and optionally may comprise at least one polymerization order. The polymer of the body. f \ 10 "Ethyl polymer" as used herein means a polymerized ethylene monomer (based on the total amount of polymerizable monomers) comprising at least 50 mole percent, and optionally may comprise At least - a comonomer polymer. The term as used herein is not used to refer to a dilute multi-block heteropolymer as described herein. "Ethylene olefin heteropolymer," By reference is meant a polymeric copolymer comprising at least 50 mole percent of polymerized ethylene monomer (based on the total amount of polymerizable monomers), and optionally at least smoke. The term used herein is not used to refer to a multi-segment heteropolymer as described herein. As used herein, "acrylic polymer," is used to mean a polymerized propylene monomer (based on the total amount of polymerizable monomers) comprising at least 5 mole percent, and optionally may comprise at least one comonomer. Polymer. The term 20 as used herein is not used to refer to an olefin multi-block heteropolymer as described herein. As used herein, "propylene/alpha-olefin heteropolymer," is used to mean at least A 50 mole percent polymerized propylene monomer (based on the total amount of polymerizable monomers), and optionally a heterogeneous copolymer of at least ~?-olefins. The term I as used herein is not used to refer to an olefin poly-insulator 171 200911847 segment heteropolymer as described herein. The term "propylene/ethylene heteropolymer" as used herein refers to a polymerized propylene monomer (based on the total amount of polymerizable monomers) comprising at least 50 mole percent, an ethylene monomer, and optionally at least one alpha- A heteropolymer of an olefin. This term is used herein to refer to an olefin multi-block heteropolymer as described herein. The term "amine-reactive group" as used herein refers to a chemical group or a chemical group which is reactive with an amine group. The term "hydroxy-reactive" or "hydroxy-reactive" as used herein, refers to a chemical or chemical group that is reactive with a hydroxy group. The term "anhydride containing compound" as used herein refers to a chemical group containing at least one anhydride group. The term "carboxylic acid-containing compound" as used herein refers to a chemical group containing at least one carboxylic acid group. The term "amine-containing compound" as used herein refers to a chemical group containing at least one amine group. The term "hydroxyl-containing compound" as used herein refers to a chemical compound containing at least one -indenyl group. The term "functionalized olefinic polymer" as used herein refers to a polymer formed from an alkene 20 hydrocarbon polymer and at least one compound, each containing at least one functional group such as an anhydride, a carboxylic acid, an amine, a hydroxyl group. Or imine. The term "amine-functionalized olefin-based polymer" as used herein refers to a polymer formed from a dilute hydrocarbon polymer and at least one compound, and at least one of the compounds contains at least one amine group. 172 200911847 "Hydroxy-functionalized olefin-based polymer," as used herein, refers to a polymer formed from an olefin-based polymer and at least one compound, and at least one of which contains at least one hydroxyl group. An imine-functionalized olefin-based polymer, as used herein, refers to a polymer formed from an olefin-based polymer and at least one compound, and at least one of which contains at least one imine capable of forming an imine. Precursor (see, for example, the following experimental examples). Test Methods Density is determined according to the American Society for Testing and Materials (ASTM) procedure ASTM 10 D792-00, Method b.

The melt index (I2) (g/10 min) was determined using ASTM D-1238-04 (version C)' conditions at 190 ° C / 2.16 kg. The designation "110" refers to the melt index (g/l 〇 minute) measured using ASTM D-1238-04, condition l90 ° C / 10.0 kg. The designation "121" refers to the use of ASTM D-1238-04, Condition 19 (TC/21.6 kg measured 15 melt index (g / l 〇 minutes). Polyethylene is basically measured at 190 ° C, while polypropylene is basically Determined at 23 (TC. MFR means the melt flow rate of the propylene-based polymer and measured using ASTM D-1238 at a condition of 230 ° C / 2.16 kg. For the amino phthalate-based polymer, including the blend containing the polymer In addition to PELLETHANETM polymer, the melt index is determined according to ASTmD-1238 condition 20 190 °C /2.16kg. For PELLETHANETM (PellethaneTM 2102-80A and 2103-70A), the melt index is 190 C according to ASTM 〇_1238 The measurement was performed at /8.7 kg. The differential scanning calorimeter (DSC) was carried out using a TAI type Q1000 DSC with an RCS cooling unit and an autosampler. Use 5 〇 "如比氮的气气173 200911847孔抓. This sample is pressed Film into a film and smelt in a press at about 175 ° C and then air cooled at room temperature (25 t). Material (3-10 mg) is then cut into 3 _ diameter wafers accurately weighed 'in __ light name (ea5Qmg) and then. The thermal properties of this sample are then detected by the following temperature profile. This sample is fast Heating to 5 180 C was maintained at isothermal for 3 minutes to remove any previous thermal history. This sample was then cooled to a thief at a cooling rate of 10 C/min and maintained at _9 ° °c for 3 minutes. This sample is then 1 〇 (: / 111111 heating to 15 〇t at the heating rate. Record this cooling and the second heating curve. The smelting temperature (Tm) is determined by the second heating curve. The crystallization temperature (Tc) is determined by the first cooling curve. 10 Final tensile strength and elongation of the fracture point are determined in accordance with ASTM D-638-03. Both measurements were taken at 231 in the die-cut D638-type IV sample. Surface tension according to ASTM D2578-04a, Method B, And DIN 53364 (1986). The ARCOTEC test ink, which is a liquid defining the surface tension, is available in the range of 28 to 56 mN/m. The test is carried out at room temperature (23 15 ° C). The ARCOTECTM test ink and test pen are available from Lotar Enterprises. At the beginning of each test, an intermediate value test ink or test pen should be used, for example, 38 mN/m (dyne/cm). The ink line stays on the material surface for at least 2 seconds 20 Changing to a droplet shape, the surface energy of the material is the same or higher than the surface tension of the liquid. In this example, a test ink/test pen having the next higher value is used to the surface, for example, 40 mN/m (dyne /cm). This test must be repeated with a higher surface tension value until the liquid line becomes the point of the separated droplet within 2 seconds. If at the beginning the droplet is formed by the liquid line as delayed 174 200911847 (38 mN/m (dyne/cm), then this test continues for the test ink/test pen with a lower value' which is usually of genius. As mentioned, the general limit is usually 32 mN/m (dyne/cm). If the surface energy level is lower than this value, the adhesion is not good. Above this value, the adhesion is good or sufficient. 5 Sheet hardness The properties are determined in accordance with ASTM D 2240-05. The tensile properties are measured according to the standard method of ASTM D638-03. The smelting tension is tested on a selected polymer sample at a Goettfert Rheotens melt tensioner at 190 ° C. This Rheotens tester consists of two In contrast, the rotating wheel consists of stretching a 10 molten strand extruded by a capillary die at a constant speed. This wheel is attached with a balancer to measure the molten stress response when the wheel is applied. This wheel accelerates until the strand breaks. The force of the rupture strand is the melt tension in centiNewton (cN). RR (V0.1 / V100) by using the melt rheology technique in an ARES (Advanced Rheometric 15 Expansion System) dynamic mechanical spectrometer (DMS) from Rheometric Scientific ) The sample was measured at 190 ° C using a dynamic frequency mode and a 25 mm (mm) diameter parallel plate fixture with a 2 mm groove. The oscillation rate was increased at 8% strain rate and from 0.1 to 100 rad/sec increments. Take 5 data points analysis at a frequency of 1 unit. Each sample (whether small particles or a pack) is compression molded at a pressure of 20,000 psi 20 (137.9 MPa) at 180 ° C for 1 minute to 3 inches ( 7.62 cm) Plates of diameter and % inch (0.049 cm) thick. The plate is quenched and cooled (more than 1 minute) to room temperature. The "25 mm plate" is cut from the center of the larger plate. These 25 mm The diameter test amount was then inserted into the ARES at 190 ° C and allowed to equilibrate for 5 minutes before the initial test. The sample was maintained under nitrogen atmosphere 175 200911847 throughout the analysis to minimize oxidative degradation. Data conversion and processing by ARES2/A5 : RSI The Orchestrator Windows 95 software package is completed. rr measures the ratio of viscosity to shear rate curve. Heterogeneous copolymer Mooney viscosity, MV, (ML 1+4 at 125. Measured according to ASTM 5 D1646-04. Rheology rate of this treatment PRR by MV and RR according to the equation PRR = RR +[3_82 - Heterogeneous Copolymer Mooney Viscosity (ML1+4 at 125 C)] χ 0.3 for the nose. ML stands for the Mani Big Rotor. The viscometer is the Monsanto MV2000 instrument. Tensile strength and elongation are measured in accordance with ASTM D-5 882-02. The sample is a squeezed sheet of 10 sheets. Tear, Type C, measured according to ASTM D-882-02. The sample is an extruded sheet. Gloss (60 degrees) is measured in accordance with ASTM D-2457-03. The sample is an extruded material. Thermal aging research. For each analysis, the sample (extruded sheet) was heat treated in a pair of 15 boxes at 120 °C (Lindberg Blue Oven, Model ESP-400C-5, pressurized air) for a period of time as illustrated in columns 9 and 10 below. After this heat treatment, the sample was equilibrated at room temperature (16 hours - 96 hours, see ASTM D573, 10.5)). Tensile strength and elongation were then measured in accordance with ASTM D-882-02. 20 Use a moisture permeability test (ASTM E 96/E 96M - 05, Inch method) Use a desiccant method to measure the moisture vapor transmission rate (MVT) and permeability. The temperature and relative humidity used for the evaluation were 72 °F and 50%, respectively. The non-laminated film was adhered to the opening of the test dish containing the desiccant and the assembly was placed under a controlled atmosphere of 72 °F and 50% relative humidity. Periodic weighing to determine the rate at which the vapor moves through the sample to the desiccant 176 200911847. 13.3 Deviation to ASTM E 96/E 96M - 05,] viVT and Permeability The MVT and permeability were multiplied by the measured film thickness to normalize to the film thickness to obtain a standardized Μ V T and permeability coefficient. This is because the permeability and MVT are directly related to the thickness of the sample and the variability of 5 degrees is derived from the manufacturing process of the film. Fourier transform infrared spectroscopy (FTIR) analysis of cis-butane diacid needle content maleic anhydride concentration is determined by the ratio of maleic anhydride at a wavenumber of 1791 cm·1 to the reference polymer peak. In Example 10 of ethylene, the reference is 2019 cm-1 per wave number. The maleic anhydride content is calculated by multiplying this ratio by an appropriate ratio of the correction constant. The equation for the maleic acid grafted polyolefin is as follows. MAH (wt%)=A*{[FTIR peak area@1791 —/[Matching area survey B*[FTIR peak area @1712cm l]/[ FTIR peak area @2〇19cm.丨]} mail”) 15 Correction The constant A can use the 13 NMR standard. The actual correction constant may vary slightly depending on the instrument and polymer used. The second component of the wave number port] cm-i illustrates the presence of maleic acid, which is negligible for the new graft material. However, during the period of time, the cis-succinic acid sulphate is easily converted to a cis-dependent surface area in the presence of moisture, and significant hydrolysis occurs in only a few days in the surrounding environment. The preparation procedure of this acid at a wavenumber of 1712 cm·1 with a distinguishable peak in the equation of the constant B in the equation between the anhydride and the acid group is corrected by a preparation procedure via a heating press at the second protective film gate p 150- 18CTC was pressed for 1 hour, and the basic thickness was made to be Q milk seal ΐ 5 mm = the beginning of the room. MYLAR and TEFl〇n are suitable protective films to protect the sample on the 25th. Never use aluminum foil (maleic anhydride and aluminum ruthenium). Ping Er 177 200911847 and under pressure (~10 tons) for about 5 minutes. The sample was cooled to room temperature and placed on a field sample of the sample. Then the cat was scanned with FTIR. The background sweeping cat must be ordered before each sample broom, or as needed. The accuracy of the test is good with an inherent difference of less than ± 5 / 〇. Samples should be stored as a desiccant to prevent excessive hydrolysis. [The moisture content in the product is determined as 0.1 weight percent, and the conversion of the anhydride to acid is reversible by temperature but may take up to 1 week for full conversion. This reversible action is best carried out at 150 ° C in a vacuum oven and requires a good vacuum (close to 3 〇 Hg). If the vacuum is below enough, the sample tends to oxidize, which results in about 174 Torr. ^^'s 1〇 infrared peak, which will cause this value to be too low. The maleic anhydride and the acid were present at peaks of about 1791 cm-i and 1712 cm, respectively. Straight iiAUL block heterogeneous copolymer 牿Zhe Shishi stop 1. Sample 1-4 and A-C GPC method Use one attached at 160. (: The automatic liquid handling machine for hot needles is added with a sufficient amount of 3 〇〇 PPm ionic alcohol (ionic alcohol) to stabilize the ι, 2, 4-tris benzene to the mother polymer without the polymer sample to obtain a final The concentration was 30 mg/mL. A small glass stir bar was placed in each tube and the sample was heated to 16 (TC for 2 hours) on a rotary vibrator rotating at 250 rpm. Concentrated polymer solution The solution was then diluted to 1 mg/ml using an automatic liquid handling machine and a hot needle set at 160 °C.

The molecular weight data for each sample was determined using a Symyx Rapid GPC system. A Gilson 350 pump with a flow rate of 2.0 ml/min was used to pump the 氦-gas scrub with 300 ppm ionic alcohol (ionic alcohol) to stabilize the 1,2-dibenzene as the mobile phase by placing three Plgel in series at 10 microns ( Μηι) mixed B 300mm X 178 200911847 7.5mm column and heated to 160 °C. A Polymer Labs ELS 100CH detector was set to 1.8 with a rotary distiller set to 250 °C, a Nebulizer set at 165 °C, and a nitrogen flow rate of 60-80 psi (400-600 kPa) N2. SLM. The polymer samples were heated to 160 ° C and each of the 5 automated liquid handling machines and hot needles were injected into a 250 μΐ loop. A series of polymer samples were analyzed using a two-switch circuit and a partial overlap injection. Sample data was collected and analyzed using Symyx EpochTM software. The peak was artificially integrated and the molecular setting was not corrected by the calibration curve of the polystyrene standard. 10 2_Standard CRYSTAF method The branch distribution was determined by crystallization analysis component action (CRYSTAF) using a CRYSTAF 200 unit commercially available from P〇lymerChar, Inc. of Vascia, Spain. This sample was dissolved in 1,2,4-trisbenzene (0.66 mg/mL) for 1 hour and at 95t for 45 minutes. The sampling temperature is between 95 and 30 ° C at a cooling rate of 15 - 0.2 ° C / min. An infrared detector was used to measure the concentration of the polymer solution. The cumulative dissolved concentration is measured by crystallization of the polymer as the temperature increases. The analytical derivative of this cumulative curve reflects the short bond branching distribution of the polymer. The temperature and area of the CRYSTAF peak can be identified by the peak analysis included in the software (Ph. 2001, PolymerChar, Vanucia, Spain). The CRYSTAF peak investigation program confirms that the peak temperature is the maximum between the dw/dT curve and the maximum forward bending line on either side of the peak confirmed in the derivative curve. In order to calculate the CRYSTAF curve, the preferred process parameters are C-threshold limits and have a temperature limit above 〇1 and a temperature limit below 〇3 179 200911847. 3. Dsc Standard Method (Excluding Samples 1-4 and A-C) The results of the differential broom calorimeter were measured using a TAI m〇del Q1000 DSC with Rcs cooling fittings and an automatic sampler. Nitrogen gas with a nitrogen of 5 〇 mi/mm was used. The sample was pressed into a film and melted in an approximate press and then cooled at room temperature (25 〇 air. The material of the 3_1 〇 mail was then cut into 6-diameter wafers, finely weighed, placed in a light _ (about 5 〇mg) and rolled up. The thermal properties of the sample were studied according to the following temperature profile. This sample was rapidly heated to 18 G ° C: ii was maintained at this temperature for 3 minutes to remove any previous thermal history of 10 samples. It was then cooled to _4 (rc and maintained at _4 〇 °c for 3 minutes at 1 TC/min cooling rate. This sample was then wl (rc/min heating rate was heated to 15 〇 ° C. Record cooling and second heating curve) The DSC melting peak is the maximum value of the thermal flow rate (W/g) for measuring the linear baseline at _3〇.〇 and the end between the melt ends. The hot melt is a linear baseline of 15 at -30 ° C and the melting end. Measurement of the area underneath 4. GPC method (excluding sample 丨_4 and aC) The gel-killing system consists of Polymer Laboratories Model PL-210 or Polymer Laboratories Model PL-220. The column and transport grid are 14 〇 C operation. Use three p〇iymer Laboratories 10-20 micron Mixed_B column. Solvent is 1,2 , 4-trichlorobenzene. The sample was prepared at a concentration of 0.1 gram of polymer in 5 liters of solvent containing 200 ppm of butylated hydroxy benzene (BHT). The sample was prepared by microstirring at 16 TC for 2 hours. The injection volume used was 1 〇〇 microliter and the flow rate was 1. 〇ml/min. The correction of the GPC column group was 2 丨 molecular weight at 580 to 8, 4 〇〇, 〇〇〇 180 180 11 200911847 The molecular weight distribution is carried out in polystyrene standards and is arranged in a 6" cocktail" mixture with at least 10 separation points between the respective molecular weights. This standard is commercially available from Polymer Laboratories (Sloza, UK). Preparation of polystyrene standards For molecular weights equal to or greater than 1, 〇〇〇, 〇〇〇 is 0.025 grams in 50 liters of 5 liters of solvent, and for molecular weight less than 1,000,000 is 0.05 grams in 50 milliliters of solvent. Polystyrene standards can be 80 °C was prepared by gentle agitation for 30 minutes. The narrow standard mixture test was first performed to reduce the highest molecular weight component to the least degradation. The polystyrene standard peak molecular weight was converted to polyethylene molecular weight using the following equation (eg in Williams and Ward, J). Polym. Sci. 10 P〇lym. Let., 6 '621 (1968)): MSw = 0.431 (M poly is "). Polyethylene equivalent molecular weight is calculated using Viscotek TriSEC software version 3.0. 5. Compressive strain compression strain Determined according to ASTM D 395. This sample was prepared by stacking 25.4 mm diameter discs having a thickness of 3 2 15 mm, 2_0 mm, and 0.25 mm until a total thickness of 12.7 mm was achieved. The wafer was cut from a 12.7 cm X 12.7 cm compression molded sheet. This sheet was molded by a hot press under the following conditions: at 190 ° C and 0 pressure for 3 minutes, followed by 190. (: and 2 minutes at 86 MPa, the conjoiner uses a running water to cool the inside of the press at 86 MPa. 2〇6. Density is used for density measurement. The sample is prepared according to ASTM D 1928. The measurement is completed after the sample is pressed using ASTM D792 Method B. 7 Flex/Cut Die/Storage Modulus Samples are compression molded according to ASTM D 1928. Flexibility and 2% secant mode 181 200911847 Measured according to ASTM D-790. Storage modulus according to astM D 5026-01 or Equal technical determination 8. Optical properties 0.4 mm Thick film was compression molded using a hot press (carver Model #4095-5 4PR1001R). The particles were placed between Teflon sheets and heated to 190 at 55 psi (380 kPa). °C was maintained for 3 minutes, then maintained at 1.3 MPa for 3 minutes, and then maintained at 2.6 MPa for 3 minutes. The film was then cooled in a press with flowing cold water at 1.3 MPa for 1 minute. This compression molded The film is used for optical metrology, tensile properties, recovery and relaxation. 10 Sharpness is measured using a BYK Gardner haze meter as specified in ASTM D 1746. 45° gloss is used in a BYK Gardner gloss meter specified in ASTM D-2457 Micro-gloss 45° measurement. Internal haze according to ASTM D 1003 Preface A is measured using a BYK Gardner 15 haze meter. Mineral oil can be applied to the surface of the membrane to remove surface scratches. 9. Mechanical properties - tensile, retardation and tear stress-strain properties in uniaxial tension according to ASTM D 1708 Micro tensile test. The sample was stretched at 500 ° min_1 with Instron at 21 ° C. The tensile strength and elongation at break were averaged from 5 samples. 20 100% and 300% delayed use ASTM D 1708 micro-tensile specimens were measured with an InstronTM instrument at periodic loadings of 1% and 300% strain. The samples were loaded at 267 o/omin·1 at 21 °C and unloaded for 3 cycles. At 300% The cycle experiment at 80 ° C was carried out using an ambience chamber. In the 8 (TC experiment, this sample was allowed to equilibrate for 45 minutes at the test temperature before the test. At 21 ° C, 300% 182 200911847 strain cycle experiment, recorded by the first The unloaded shrinkage stress is at 150% strain. The percent recovery from all experiments is calculated from the strain of the first unloaded cycle using the load back to the black line. The percentage of recovery is defined as follows: %Revert = • ε/ 5 where sf is the strain of the periodic load and Es is loaded back to the base during the first unloaded period Line strain. Stress relaxation was measured using an InstronTM instrument with an ambience chamber at 5 〇 Γ strain and 37° 0 12 hours. The geometry of this measurement dimension is 76 mm X 25 mm X 0.4 mm. After equilibrating for 45 minutes at 37 ° C in the ambience chamber, the sample was stretched to 50% strain at 10 333 ° ^ ^ ^ 1 . The stress is recorded as a function of 12 hours. The percentage of stress relaxation after 12 hours was calculated using the following formula: % stress relaxation = ^f^xl00 where L〇 is the strain at 50% 0 time load and the load at 1212 after 12 hours is at 50% strain. The 15 dent dent tear test was performed using an InstronTM instrument with a sample having a density of 0.88 g/cc or less. This geometry consists of a measuring size of 76 mm X 13 mm X 0.4 mm with a 2 mm indentation cut into the sample half the length of the specimen. This sample was stretched at 211 at 508 mm/min until breaking. The tear energy is calculated as the stress-elongation curve up to the surface of the strain of the maximum load. Report on the average of at least 3 samples.

10. The TMA thermomechanical analysis (penetration temperature) was carried out on a compression molded disc of 3 mm mm diameter x 3.3 mm thickness 183 200911847, which was carried out under 丨8〇 and 1〇Mpa molding pressure. Minutes and then quenching to form the instrument for 吏7, which is a brand available from Perkin-Elmer. In the test, -1) ΓΪ1ΓΤ1 The tip of the radius probe (P/N N519_0416) was applied to the surface of the sample on the surface of the sample at a force of 1 N. The temperature rises from 25 C at 5 C/min. This probe penetration distance is measured as a function of temperature. The experiment was terminated when the probe penetrated to the sample 丨mm.

11. DMA Dynamic Mechanical Analysis (DMA) was measured on a compression molded wafer which was formed at 180 ° C for 5 minutes at 10 MPa and then cooled at 9 Torr / 10 minutes in a press. The test was performed using an ARES controlled strain rheometer (Texas Instruments) with a dual cantilever holder for torque measurement. A 1.5 mm sheet was pressed and cut into a rod shape of 32 X 12 mm. The two ends of the sample were clamped between holders with a pitch of 10 mm (clamping pitch a) and subjected to a continuous temperature step from -100 ° C to 200 ° C (each step 5. 〇. at each temperature of 15 degrees 'torque mode) The G' angular frequency is measured at 10 rad/s and the strain amplitude is maintained between 〇j and 4% to ensure that the torque is sufficient and the measurement is maintained in a linear solution. Maintain a starting friction of 10 g (automatic tension mode) to prevent When thermal expansion occurs, the sample is loose. Therefore, the grip separation AL increases with temperature, especially above the melting or softening point of the polymer sample. This test is at the highest temperature or 20 when the groove between the two holders has reached 65 mm and stops. 12. The melt index or Is of the melt index polyethylene polymer is measured according to ASTM D 1238 condition 190 ° C / 2.16 kg (polypropylene polymer condition is 230 C / 2.16 kg). The smelting index or Iio sometimes Measured in accordance with ASTM D 1238 conditions 190 ° C / 10 kg. 184 200911847

13. ATREF analysis of temperature rise elution component effect (ATREF) analysis is based on US Patent No. 4,798,081 and Wilde, L.; Ryle, TR; Knobeloch, DC, Peat 'IR, Determination of Branching Distributions 5 in Polyethylene and Ethylene Copolymers, J. Polym. Sci., 20, 441-455 (1982), the method described, which is incorporated herein by reference. The analyzed composition was dissolved in tri-gas benzene and slowly lowered to a temperature of 20 ° C at a cooling/min cooling rate to allow crystallization in a column with an inert support (stainless steel shot). This column is attached with an infrared detector. A 10 ATREF chromatogram curve was then generated by eluting a crystalline polymer sample at a rate of i 5 ° C/min from the column at a rate of 2 Torr to 120 ° C to slowly increase the temperature of the eluting solvent (three gas stupid). 14.13 C NMR Analysis Approximately 3 g of a 50/50 tetrachloroethane-d2/o-halo 15benzene mixture was added to a 0.4 g sample in a 10 mm NMR tube to prepare a sample. This sample was dissolved and homogenized by heating the tube and its contents to 150X:. Data was collected using a je〇L EclipseTM 400MHz spectrometer or a Varian Unity PlusTM 400MHz spectrometer, equivalent to a 13C resonance frequency of 100.5 MHz. Data was acquired for each data using a 4 〇〇〇 transient with a 6 second pulse repetition delay. In order to obtain a minimum amount of analysis noise, multiple data pieces are added together. The spectral width is 25,000 Hz' with a minimum data size of 32K data points. The samples were analyzed in a 10 mm wide-band probe at 丨川乞. The comonomers were determined using the Randall's triad method (Randall ' JC; JMS-Rev. Macromol. Chem. Phys., CM, 201-317 (1989), which is incorporated herein by reference. 185 200911847 15. TREF The polymer component acts as a large-scale TREF component by 15-20 g of polymer via a 丨6 (rc for 4 hours to dissolve in 2 liters of 1,2,4-trichlorobenzene (TCB). Polymer solution Pushed at 15 psig (100 kPa) nitrogen into a 3 inch x 4 inch (7.6 cm x 12 cm) fill 60:40 (v: v) mixed 30-40 mesh (600-425 μπι) spherical, technical quality Glass beads (available from Potters Industries, HC 30 Box 20, Brown Forest, TX 76101, USA) and stainless steel 〇〇 28" (0_7 mm) diameter steel wire pellets (Pellets, 63 Industrial Avenue, North Tannawa, New York, USA 14120, USA) The steel pipe is obtained by impregnating the oil jacket of a heat control 10, initially set to 160 ° C. The pipe column is rapidly cooled to 125 ° G, then slowly cooled at 〇 〇 4 ° C per minute. It was maintained at 20 ° C for 1 hour. Fresh TCB was added at about 65 ml/min while the temperature was increased at 0.167 ° C per minute. Approximately 2000 ml of the extract was collected from the prepared TREF column at 16 points, and the component collector was heated. The polymer was concentrated in each component with a rotary evaporator until about 50 to 100 ml of the polymer solution remained. This concentrated solution is allowed to stand overnight before adding excess sterol, filtering and rinsing (about 300-500 ml of methanol, including the final rinse). Filtration step at a 3-position vacuum assisted transition station using 5.0 μιη Tetrafluoroethylene coated paper (available from Osmonics, Cat# Z50WP04750) was passed. The transition was dried in a vacuum oven at 60 ° C overnight and weighed on an analytical balance before further testing. 16. Melt Strength The melt strength (MS) is measured using a capillary rheometer equipped with a 2.1 mm diameter 20:1 die with an entry angle of approximately 45 degrees. At 19 (TC after equilibrium sample 186 200911847 10 minutes later 'to 1 The piston was operated at a speed of 吋/min (2.54 cm/min). The standard test temperature was 190 ° C. This sample was uniaxially stretched with a set of acceleration clamps of 2.4 mm/sec 2 acceleration at 1 〇〇 mrn below the die. Record the demand for tensile Sandwiched roll-off rate of the hole of the lead. 5 ultimate tensile force obtained during the test is defined as the melt strength. In the example where the polymer melt exhibits tensile resonance, the tensile force before the tensile resonance is initiated is regarded as the smelting strength. The melt strength is recorded in centiNewtons ("cN").

EXAMPLES The following examples are intended to illustrate the invention and are not intended to be exhaustive or to be construed as limiting. The following components were used in the following examples. PELLETHANETM 2102-80A is a thermoplastic polyurethane having a density of 1.18 / (^ (8 3 ) 〇 792) and at 190. (4 g/10 min measured at 8.7 kg) Melt index (12) (available from Dow Chemical Company). PELLETHANETM 2103-70A is a thermoplastic polyamino phthalate having a density of 1.06 § / (^ (8 3 ]) 〇 792) And at 190° (: 11 g/10 min melt index (12) measured by 8.7 kg (available from The Dow Chemical Company). 20 PELLETHANETM 2355-80AE is a thermoplastic polyurethane with 1.18§/(^(八三丁)^〇792) Density, and at 190° (: 7 g/10 min melt index (12) measured by 8.7 kg (available from The Dow Chemical Company). PELLETHANETM 2103-80AEF is a thermoplastic polyurethane 187 200911847 ester having a density of 1.13 g/cc (ASTM D 792) and a melt index (〗 2) of 13 gH〇min measured at 190 ° C at 8-7 kg ( Available from The Dow Chemical Company. AMPLIFYTM GR-216 is an ethylene/octene-1 copolymer with about 0.88 wt% maleic anhydride with 0.875 g/cc (ASTM D 792) ) density, and 1.3 g /10 min melt index (〗 2) (available from The Dow Chemical Company). AFFINITY-g-AMINE is also known as AFFINITYGA1950-g-amine or AFFINITYGA-g-amine, which has a density of 0.87 g/cc. And a maleic anhydride-grafted AFFINITY GA 1950 resin having a maleic anhydride content of 0.7 wt% 10 was reacted by inhalation of 2 molar equivalents of ethylethylenediamine followed by melt mixing by a small REX extruder. Affinity GA1950 resin is a particularly low-volume low molecular weight resin whose basic characteristics are viscosity rather than melt index. The Brookfield viscosity of the resin before ΜΑΗ grafting is 177 15 . (: 17000 cps (as ASTM D 1084) 8407-g-MAH was prepared by reacting ENGAGETM 8407 ethylene-octyl acrylate with a density of 0.87 g/cc and a melt index of 30 with maleic anhydride. The final melt index is close to 5 and cis. The dibasic anhydride content is close to 8.8 wt%. 20 8402-g-amine is grafted by 〇.8 wt% MAH ENGAGETM 8402 (density = 0.9, MI = 30 before grafting, river 1 after grafting = 5) by first inhaling 2 moles of ethylethylenediamine and then passing the accepted small particles through a REX Press. AMPLIFYTM GR216-g-amine is also known as AMPLIFY GR216 188 200911847 Maleic anhydride (ΜΑΗ) graft polymer, available from The Dow Chemical Company, with 1.25 ΜΙ, density 0.87, graft content 0.8 wt %, which inhaled 2 mole equivalents of ethylethylene diamine (DEDA) and then melt blended in a reactive extruder. 5 LDPE 662i is a low density polyethylene with a density of 0.917 g/cc and a melt index of 0.47 (190 C/2.16 kg) available from The Dow Chemical Company. VERSIFY 2000-g-DEDA was prepared from a VERSIFYTM 2000 propylene-ethylene copolymer grafted with 0.9 wt% MAH having an ethylene content of 5 wt%. The starting VERSIFY copolymer has an MFR of 2 (230 C/2. 16 kg) and a density of 10 0.888 g/cc. The ruthenium graft is converted to a ruthenium amine by reaction with 3 molar equivalents of ethylene diamine. . OBC 9817_10-g-amine consists of 1.17% ΜΑΗ grafted D9817.10 Developmental olefin block copolymer (density = 877 877, 3.04 ΜΙ) by reaction extrusion using 3 molar equivalents of ethyl ethylene diamine be made of. 15 OBC 9807.10-g-amine D9807.10 Developmental olefin block copolymer (density = 〇 866, 3.80 MI) grafted from 1.13 wt ° / 藉 by using 3 molar equivalents of ethyl ethylene diamine It is prepared by reaction extrusion. OBC(32MI)-g-amine is grafted by 1_〇9 wt% 〇 BC (density = 0.877, 7.08 ΜΙ) by using the anti-20 squeezing effect of 3 molar equivalents of ethyl ethylene diamine. be made of. The sample labeled 8407-g-amine (Α) is ENGAGETM 84〇7 _g_(2_[N_ethylamino]butylbutylimine (0.87 density; ~5 smelting index) and has the following structure. Branch polymer by grafting maleic anhydride to Engage 84〇7 (0·87 post, degree, 5 MI) material (~0.74 wt% ΜΑΗ graft amount) and butyl 189 200911847 ethylene diamine use 2 This is obtained by reacting an equivalent of a diamine/anhydride. This diamine is inhaled into small particles and passed through a small REX extruder.

8407-g-amine (B) is ENGAGETM 8407-g-(2-[N-ethylamino]-5 ethylbutadiimide (0.87 g/cc density; about 5 melt index; 1.2 wt% [ N-ethylamino]ethylbutadiimide) and having the structure of the following reaction scheme A. The graft polymer was grafted with cis-butyl dianhydride to Engage 8407 (0.87 g/cc density, 5 g/10 min MI, about 0.74 wt% ΜΑΗ graft amount) was prepared by reacting ethyl ethylene diamine with 2 equivalents of diamine/anhydride. This diamine 10 was inhaled with maleic anhydride grafted EngageTM 8407. Small particles, and the inhaled particles are melt blended in a small REX extruder.

(Reaction diagram A) 8407-g-OH is ENGAGETM-g-(2-hydroxyethylbutadiimide) (0.87 g/cc density; about 5 g/ΙΟ minutes of thawing index; 1.0 wt% by base 15 butyl bisimide), and the graft polymer was grafted with maleic anhydride by Engage 8407 (0.87 g/cc density, 5 g/ΙΟ min MI, about 0.74) in a small extruder. The wt% Μ AH graft amount) was prepared by reacting ethanolamine with 3.5 equivalents of ethanolamine/anhydride. The reaction is shown in the following Reaction Scheme B. 190 200911847

8407-g-DEDA refers to ENGAGETM 8407 grafted with about 5 wt% ruthenium having a density of 5 MI and 〇.87 g/cc, which is then used with 3.0 moles (5 ethylene ethyl diamine (DEDA)). Conversion to a ruthenium amine in a reactive extruder. AMPLIFYTM GR216-g-DEDA refers to an AMPLIFY GR216 maleic anhydride (ΜΑΗ) grafted polymer with a density of 1.25 MI, 0.87 and 0.8. The grafting content of wt%, which is then converted to the ruthenium amine in a reactive extruder using 3.0 molar equivalents of ethyl 10 ethylene diamine (DEDA), available from The Dow Chemical Company. OBC 9817.10-g -Amine was prepared from 1.17% ΜΑΗ grafted D9817.10 I, Developmental Hydrazine block copolymer (density = 0.877, 3_04 ΜΙ) by a reactive extrusion process using 3 mole equivalents of ethyl ethylene diamine. 15 D9507 Developmental dilute hydrocarbon segment copolymer is an ethylene/octene-1 multi-block copolymer with a density of 0.866 g/cc and a melt index of 5 g/10 min (12) (available from The Dow Chemical Company). 00 Developmental olefin block copolymer is an ethylene/octene-1 multi-block copolymer having a density of 0.877 g/cc and 0.5 g/10 Min melting 20 melting index (12) (acquired by Dow Chemical Company) 191 200911847 D9500 Developmental olefin block copolymer is a mixture of ethylene/Mulberry-1 Doxin, with a density of 0.877 g/cc and 5 g/i 〇 指数 index (12) (available from The Dow Chemical Company) FUSABOND 493D is a cis-butyl; 5 total t-materials with 〇·87 g/cc selectivity and 1.2 melt index (12) (19 〇C/2·16kg), available from DuPont. The extruded sheet contains the extruded sheet of the composition labeled A-Ι in Table 6 below by 140°C in zones 1 to 4 of zsk-25, respectively. , 170 ° C, 170 ° C and 1702⁄4 》, 曰 10 degree curve combined with this composition to produce. The resulting composition is then dried and used 175 ° C, 185 ° C, 190 ° C temperature curve and equipment The Maddock Hybrid Spiral Killion three-sheet production line is extruded into 20 ml thick sheets. Table 6 Component A wt% B wt% C wt% D wt% E wt% F wt% G wt% H wt% I wt% OBC 9000 84 73.3 60.5 58 53 60.5 60.5 60.5 60.5 PELLETHANE -. 2103-70A 0 25 37 37 37 37 0 0 0 PELLETHANE 〇2355-80AE U 0 0 0 0 0 0 0 37 PELLETHANE 〇2103-80AEF U 0 0 0 0 0 0 37 0 PELLET HANE Λ 2102-80A υ 0 0 0 0 0 37 0 0 AMPLIFY GR216-g-DEDA 1 U 1.7 2.5 5 10 0 2.5 2.5 2.5 OBC 9817.10 -g-AMINE 0 0 0 0 0 2.5 0 0 0 Total 100 100 100 100 100 100 100 100 100 Tested on a sheet labeled A-Ι, the results are shown in Table 7. 192 15 200911847 Table 7 Test ABCDEFG Η I Membrane average of 60°-5 readings (〇/0) 10 7 23 14 13 19 31 18 14 _Tear: Thermoplastic TypeC-CD average tear strength (lbf/ In) 264 253 236 269 308 181 315 320 312 Tear: Thermoplastic TypeC-MD average tear strength (lbf/in) 269 290 280 286 304 253 370 390 372 Tensile-CD-D638 stress at break (psi) 1708 1201 1893 2805 2640 1626 2575 2140 2567 Average strain (%) of tensile-CD-D638 at break 911 746 744 630 812 740 638 681 589 Average stress (pSi) of tensile-MD-D638 at break 2580 2435 2785 2351 3366 2588 3961 3464 4168 Tensile-MD-D63 8 Average strain @BRE AK(%) 589 623 751 814 721 686 661 599 592 Surface energy (dyne/cm) 34 34 34 34 34 34 30 34 34 United Coating's PU Coating AWOF-0082 Coating Cross-Paint Bonding Test Rating (Score) 5 5 5 5 5 5 5 5 5 "Dow Great Stuff Insulation Foam"Adhesive ίBinder Failure)(PASS/ Failure) failure failure through failure by passing through the composition of the label JQ included in Table 8 below The extruded sheet by zsk-25 in zones 1 to 4 are 140 ° C, this compound under the temperature profile 170 ° C, 170 ° C and 170 ° C of the compositions prepared. The resulting composition was then dried and 5 extruded using a 175 ° C, 185 ° C, 190 ° C temperature profile and a Maddock hybrid spiral phantom 11 丨〇 11 three-sheet production line into 2 〇 1111 thick sheets. Table 8 Component J wt% K wt% L wt% M wt% N wt% O wt% P wt% Q wt% OBC 9000 84 73.3 60.5 58 53 60.5 60.5 60.5 PELLETHANE 2103-70Α 15 25 37 37 37 0 0 0 PELLETHANE 0 0 0 0 0 0 0 37 2355-80AE PELLETHANE 0 0 0 0 0 0 37 0 2103-80AEF PELLETHANE 2102-80A 0 0 0 0 0 37 0 0 AMPLIFY GR216-S-MA 1.01 1.7 2.5 5 10 2.5 2.5 2.5 Total 100 100 100 100 100 100 100 100 Tested on a sheet labeled JQ, the results are shown in Table 9. 193 200911847 Table 9 Test JKL Μ Ν 〇Ρ Q Membrane average of 光泽60°-5 readings (〇/〇) 18 22 20 31 28 25 10 15 Tear: Thermoplastic TypeC-CD average tear strength (lbf/ In) 250 254 251 275 293 338 258 304 Tear: Thermoplastic TypeC-MD average tear strength (lbf/in) 252 299 327 295 290 380 386 420 Tensile-CD-D638 stress at break (pSi) 2307 2283 2088 2806 2763 1543 1506 1819 Tensile-CD-D63 8 average strain at break (〇/〇) 822 833 743 815 826 564 542 485 Tensile-MD-D638 average stress at break (pSi) 2914 3719 3254 3597 3496 4123 2805 3693 Tensile-MD-D638 average strain @31^^(%) 710 769 623 768 756 455 532 434 Surface energy (dyne/cm) 34 34 34 34 34 30 35 32 PU from United Coating Cross-coating adhesion test score for coated AWOF-0082 coating (score) 3 5 5 5 5 5 5 5 Adhesion of "Dow Great Stuff Insulating Foam" _ (Adhesion failure) (pass/fail) Failure failure through Passing through by passing the extruded sheet containing the composition of the label RW in Table 10 by means of the middle zone in zsk-30 1-4 are 140 ° C, this compound under the temperature profile 170 ° C, 170 ° C and 170 ° C of the compositions prepared. The resulting composition was then dried and 5 extruded using a 175 ° C, 185 ° C, 190 ° C temperature profile and extruded into a 20 ml thick sheet using a %" Haake extruder. Table 10 Component R wt % S wt % T Wt% U wt% V wt% W wt% OBC D9000 51.75 50.5 48 0 0 60.5 OBC for rheological modification (70wt% OBC 9100 and 30 wt% DS6D82 with Ding 1^〇11〇\1〇丨15〇(^ 0111 and Coagent SR 350 1500 ppm) 0 0 0 60.5 0 0 BC for rheology modification (OBC9100 #Trigonoxl01 lSoOppm and Coagent SR350 1500 ppm) 0 0 0 0 60.5 0 LDPE 662i 10 10 10 0 0 0 PELLETHANE 2103-70A 37 37 37 37 37 37 AMPLIFY GR 216 1.25 2.5 5 2.5 2.5 2.5 Total 100 100 100 100 100 100 194 200911847 Tested on a sheet labeled RW, the results are shown in Table 11. Table 11 Test RSTUVW gloss 60 degrees - Membrane average of 5 readings (%) 13.6 15.58 7.94 15.64 4.76 6.68 Tear: Thermoplastic TypeC-CD average tear strength _ (lbf/in) 224 241 282 313 230 243 Tear: Thermoplastic TypeC-MD average tear Strength (lbf/in) 343 509 658 1096 530 635 Tensile-CD-D638 stress at break (psi) 238 334 363 500 335 496 -CD-D63 8 average strain at break (%) 35 35 35 35 35 35 Tensile-MD-D638 average stress at break (psi) 5 5 5 5 5 5 Tensile-MD-D638 average strain ( ® y BREAK (%) By studying the composition of the invention in the following table by passing the failure through the injection molding sheet 5, the composition in the following table is blended with 5 weight percent of the functionalized polyolefin and the olefins of different weight percentages and types by blending the total composition Polyblock copolymer (OBC) 'SBS 401, and thermoplastic polyurethane. Thermoplastic polyurethane (TPU) is a polycaprolactam polyester with methylene diisocyanate An alcohol-based TPU having a density of 1.18 g/cm 3 , 5 g/10 min of 10 MFR (190 ° C / 2.16 kg), and a Shore A hardness of 80. SBS 401 was prepared from Total Petrochemicals having a styrene-butadiene weight ratio of 22: 28 wt% and a density of 0.93 g/cm3. The functionalized polysulfonate is a reactive extrusion of 8407-g-amine based on the reaction of Engage 8407 (-0.8 wt% ΜΑΗ, MI 〜5) grafted with 莫15 molar equivalent ethylethyldiamine. And made. The OBC used in samples 2 and 6-8 in the following Table 12 is OBC 9100, and the samples used in samples 3-5 and 9-10 are OBC 9500. 195 200911847 Table 12 OBC (wt%) SBS 401 (wt%) TPU (wt%) 1 40 0 55 2 0 60 35 3 40 0 55 4 0 40 55 5 25 25 45 6 0 40 55 7 60 0 35 8 25 25 45 9 0 60 35 10 60 0 35 In the above table, the composition of the present invention can be injection molded into a sheet on an injection molding apparatus, substantially about 0.5 to 1 cm thick, which is basically used in the footwear industry. The injection molding is carried out at a suitable melting temperature (substantially about 160-170 5 ° C), a suitable molding temperature (substantially about 60-80 ° F), and a suitable ejection speed. The properties are shown in Table 13. Table 13 Sample Hardness Density Load at break Prolonged Wear Tear Melt Index Xiao's A g/cc Kg/cm2 % mm3 Kg/cm 15 1 73 1.001 17.8 1131 201 43 36 2 63 1 9.9 928 178 37 1.1 3 76 0.991 12 867 197 51 5 4 68 1.048 12.8 922 96 45 4.5 5 72 1.008 10.4 874 164 44 5.7 6 67 1.048 15.3 1056 107 44 4.6 7 75 0.983 9.2 1158 332 43 2.8 8 69 1.004 14.6 1055 179 37 4.8 9 65 1.002 6.6 705 143 30 1 10 77 0.968 6.3 817 179 42 8.6 196 200911847 Injection molding-combination blend and "blend in press" Blend blending on Werner & Pfleider zsk-25 compounding extruder to prepare blend . Prior to compounding, the TPU and polyolefin feeds are fed through a separate weight loss feed which controls the feed ratio of the desired composition. AMPLIFYTM GR216, Polybd 2035 or Grafted Amine Polymers are blended with polyolefins. This extruder was operated at 1 rpm of the total flow rate in lb/hr. In one embodiment, the extruder has an rpm of 500 for a total flow rate of 50 lbs/hr. A temperature curve of 140 ° C was used in zone 1 and a temperature curve of 17 CTC was used in zones 2 to 8. When the extruder is discharged, the extruded strands are granulated to form a compounded pellet. The blend formulation is shown in Table 14 below. The olefin block copolymer developed by D 9500 is an ethylene-octene block copolymer having a crucible of 2.16 kg and a density of 0.877. PELLETHANETM 2103-70A is a thermoplastic polyurethane 15 ester having a density of 1 〇 6 g/cc (ASTM D 792) and a melt index of 19 g (11 g/10 min measured by TC at 8.7 kg). (l2) (available from The Dow Chemical Company). AMPLIFYTM GR216 is a grafted acetamethylene-octene copolymer having a MI of 1 and a density of 0.87. 20 Polybd 2035 is a polybutadienyl TPU. It has a Tg of -34 〇C, a specific gravity of 0.995 g/cc at 25 ° C, a tensile strength of nil pSi, a ι 2 of 1 g/ΙΟ minute, a hard segment content of 35 wt%, and a softening point of 90. (: and 559% extension (obtained by Sartomer). .8407-g-AMINE refers to 197 200911847 ENGAGETM 8407 which is grafted to 〇.8 wt% with MI of 5 and density of 0.87 g/ Cc, followed by conversion to the acid imidized amine in a reactive extruder using 3.0 molar equivalents of ethyl ethylene diamine (DEDA). Table 14: Blend Formulation 46 47 48 49 50 0BC 9500.00 65 60 60 60 65 PELLETHANE 2103-70A 35 35 35 35 30 Polybd 2035 0 5 0 0 5 AMPLIFY GR216 0 0 5 0 0 8407-g-Amine 0 0 0 5 0 5 The blend in the press is shown in the table below The blend of 15 was dry blended and injection molded in the history of the press without any compounding steps. Table 15: Blend formulation in the press 51 52 53 54 55 56 57 OBC 9500.00 65 60 60 60 65 100 0 PELLETHANE 2103-70A 35 35 35 35 30 0 100 Polybd 2035 0 5 0 0 5 0 0 AMPLIFY GR216 0 0 5 0 0 0 0 8407-g-Amine 0 0 0 5 0 0 0 Injection molding example 10 at ARBURG 370C- Injection molding was carried out in an 80 ton injection molding machine. The basic injection molding conditions of the blend blend and the blend molded in the press are shown in Table 16. 198 15 200911847 Table 16: Injection molding conditions in the press In the compound 41; 1/16" sheet and 1/8" Μ柘 compound 46; (4x6xl/16"4x6x0.0625" barrel and mold temperature zone 1 temperature T801 (〇F) 250 250 zone 2 temperature T802(°F) 350 350 Zone 3 Temperature T803 〇Τ) 375 392 Zone 4 Temperature Τ 804 (°F) 375 392 Nozzle Temperature T805 (°F) 375 392 Die Temperature (°F) 70 65 Extruder RPM v401 (m /min) 10 30 After pressure p401 (bar) 75 15 Dose V403 (ccm) 45/70 45/70 Real dose V403 (ccm) 47/72 47/72 Most Injection injection speed #1 __Q301(ccm/s)__ 30 10 Conversion position V311 (ccm) 15 12 Conversion pressure p358I (bar) 1109/610 825/383 Filling time t3 05m (seconds) 1.19/2.01 2.3/3.83 Buffer V3211 (ccm) 9.5/7.1 5.6/3.2 Continuous action pressure #1 p321 (bar) 400 600/390 time - duration #1 t321 (seconds) 30 30 cooling time t400 (seconds) 20 20 dose time t402m (seconds) 14.2/23.3 ___8.7/11.2 Cycle time t902 (seconds) 57.7/62.5 .___ 59/59.5 The wear test used is in accordance with ASTM D 1242, however, the samples are worn with different types of grinding wheels in a TABER wear device. The resulting weight loss is measured and presented as a percentage of weight loss. Tensile testing was performed at 20 in/min according to ASTM D 638. The tensile stress, elongation and toughness at break were respectively measured in this test. The Shore A hardness is measured in accordance with ASTM D2240. This test method allows for the measurement of hardness at the beginning of the most 199 200911847 indentation or indentation after a certain period of time or both. In this case, a specific time of 5 seconds is used. Tearing _ Gull Wing is determined according to ASTM 〇 1004. This test primarily measures the force of the initial tear. 5 Flexural modulus is determined in accordance with ASTM D 790. This test measures the flexibility or bending properties of the sample. Testing using the "DOW GREAT STUFF" foam was also carried out. This test was carried out by bending a "2" diameter disc on a blown film with a small rectangular tape tab bonded at 1 cm of the diameter edge to bend overnight. In this sample, the adhesive tape or the failing property of the adhesive of 5 pieces of the foam was adhered by hand. A pure polyolefin sample of a control group showed no foam adhesion or residue. The physical properties of the compounded blends are shown in Table 17 below. The physical properties of the blend of presses are shown in Table 18 below. TableΠ: Physical properties of compound blends 46 47 48 49 50 Wear modification % weight loss 4.5 6,1 3.3 3.9 5.9 Wear standard deviation 0.2 0.1 0.1 0.1 0.1 Flexible modulus average flexural modulus ksi 2.4 1.9 2.1 2.3 2.1 Standard deviation of flexible modulus ksi 0.4 0.2 0.0 0.1 0.0 Hardness type _ A-5 seconds 5 readings average 66.7 61.6 72.1 70.6 64.2 Standard deviation of 5 readings 1.0 0.5 0.5 0.6 0.5 Tearing - Gull Wing Average tear strength lbf/in 188.1 154.0 215.8 215.2 162.7 Standard deviation of tear resistance lbf/in 4.7 11.4 1.3 2.5 2.7 Average strain % of tensile at break 1084.2 604.8 747.8 643.0 757.6 Average stress at break psi 1130.8 879.9 1538.3 1034.5 910.0 Mean tenacity in*lbf 158.7 68.2 112.6 80.4 89.2 Standard deviation of strain at break % 246.2 129.1 54.6 46.2 114.2 Standard deviation of stress at fracture 0 psi 89.5 90.6 231.7 37.7 64.6 Standard deviation of a toughness in*lbf 41.9 19.0 14.5 6.4 13.8 200 200911847 Table 18: Physical properties of the blend of presses Unit 51 52 53 54 55 56 57 Wear modification % weight loss 5.4 5.5 4.1 2.7 5.7 0.6 0.0 Flexural modulus wear standard deviation ksi 0.0 0.1 0.0 0.1 0.0 0.1 0.1 _ Average flexural modulus 2.7 2.7 2.9 2.7 3.1 3.8 2.3 Hardness type Α-5 seconds Standard deviation ksi 0.5 0.1 0.4 0.3 0.7 0.1 0.3 5 The average number of readings is 73.0 71.9 73.3 74.1 72.9 72.6 71.0 The standard partial reading of 5 readings is 0.6 0.3 0.1 0.3 1,2 0.3 0.3 The average tensile strength of the crack should be quite 56. 915.1 576.8 676.7 529.3 508.0 603.9 In the break ~~ Psi 1021.7 1183.3 1309.2 1296.6 1063.6 945.7 3108.5 Average tenacity in*lbf 65.8 116.7 71.7 88.7 60.0 56.5 82.7 Low standard of strain at break # % 309.6 418.2 237.2 39.2 306.2 35.0 80.1 Standard pseudo-bar psi at fracture stress 49.4 157.3 169.0 162.9 161.4 46.7 157.3 Standard deviation of toughness in*lbf 37.0 56.2 37.6 6.3 41.0 5.6 24.1 tearing _ Gull Wing average tearing Min 274.3 225.2 235.1 245.0 226.3 204.7 364.4 Standard deviation of tear resistance lbfi^in 17.9 12.7 4.6 7.8 4.8 4.4 21.6

Samples of amine grafted or ruthenium graft compatibilizers provide the best balance of properties. All samples were tested for foam failure (both compound and pressed material) in the foam test, indicating that the blend is useful in bonding applications. 5 needs to be bonded to polar polymers such as PC, ABS, PET, and resistant. s. - This application is overpressure molding. Blends of OBC and TPU with amine graft polymers as compatibilizers have better toughness properties than pure OBC or TPU. Compositions containing an amine graft polymer or a ruthenium graft polymer provide a good balance of properties. A overpressure molding

10 Polycarbonate CALIBRE, ISOPLAST processing mT, i PU, resistance to CAPRON, or MAGNUMABS overpressure molding on one of the "compound blend 51_55, or "Human figure 46-50" can not be Hand-peeled component, and "Control 56 pure OBC" produces an overmolded component that can be easily peeled off by hand ^ ISOPLAST 2530 is a processing heat 15 plastic polyamine phthalate available from The Dow Chemical Company. ^ 201 200911847 CAPRON is a polyamine (available from BASF). CALIBRE 200-14 is a polycarbonate available from The Dow Chemical Company. MAGNUM 3325 ABS is available from The Dow Chemical Company and has a 1_05 g/cc The density and the melt flow rate of 10 g/10 min (220 ° C / 10 kg). The "in 5 press" and the combined injection molding blend showed excellent adhesion to PU foam. This blend has excellent properties. Mechanical properties. "In presses, blends and compound blends can be overmolded with polar polymers such as PC, ABS, nylon, ISOPLAST. These blends have comparable toughness relative to pure τρυ. Blending of Blown Film 10 Blend The blend was prepared on a Werner & Pfleider zsk-25 compounding extruder. Prior to compounding, the TPU and polyolefin are fed through a separate weight loss feeder that controls the feed ratio of the desired composition. AMPLIFYTM GR216 and LDPE are fed together with the dry blend of polyolefin. This extruder was operated at 1 rpm rpm with a total flow rate of ib/hr for a single 15 bit. In one embodiment, the extruder has an rpm of 500 for a total flow rate of 5 lbs/hr. A temperature profile of 140 ° C was used in zone 1 and a temperature profile of 170 ° C was used in zones 2 to 8. When the extruder is discharged, the extruded strands are granulated to form a compounded pellet. The blend formulation is shown in Table 19 below. Table 19 38 39 40 41 42 43 44 45 OBC 9000 57.48 55.05 52.50 54.60 52.35 50.09 48.10 ENR 7086 57.48 PELLETHANE 2103-80AEF 35.15 35.15 35.15 35.15 35.15 35.15 35.15 35.15 AMPACET 10063 5.00 5.00 5.00 5.00 5.00 5.00 5.00 5.00 LDPE 50 li 4.98 LDPE 132i 2.87 2.76 2.64 7.00 AMPLIFY GR216 2.38 4.80 2.38 2.38 2.38 4.75 7.13 4.75 100.0 100.0 100.0 100.0 100.0 100.0 100.0 100.0 202 200911847 D 9500 developed olefin block copolymer with a MI of 5 (190 C, 2.16 kg), density = 0.877 An ethylene-octene block copolymer. PELLETHANETM 2103-80 AEF is a polyether diol TPU with a density of 1.13 g/cc (ASTM D 792) and a melting index (I2) of 13 g/10 min (190 ° C / 8.7 kg) ). AMPACET 10063 is a primary-block primary batch having 25% yttrium oxide in the LDPE carrier obtained from Americhem. LDPE 50 is an LDPE obtained by The Dow Chemical Company having a density of 0.922 and an MI of 1.9 (190 ° C / 2.16 kg). 10 LDPE 132i is a LDPE obtained by The Dow Chemical Company, which has a density of 0.92 and an MI of 0-25 (19 (TC/2.16 kg). In]^1^丫7乂11216 has a density of 1^1. 〇.87§/(^ ΜΑΗ grafted ethylene-octene copolymer. Also includes a high melt strength ENR 7086 ethylene-butene copolymer ratio 15 compared to the example, which has a density of 0.9 g / cc and ΜΙ 0.3. Blown Film Example The blown film was implemented on a DR Collin co-extruded film line consisting of three extruders, a die, a cooling ring with chilled air, a pinch roller, and a collection of the film. The extruder is 25mm, 30mm and 25mm with 25: 20 L/D. The die gap can be exchanged in 1.〇, ι·4 and 2, for example. The die diameter is 60mm. The output rate depends on the resin properties. Between 4 kg and up to 20 kg/hr. Only a single layer structure was produced in this study. The temperature profile used in this study was 165, 170 in the regions 1 to 4, the joints and the die. 175, 180, 185 and 190t and a thickness of 2.5 m 203 200911847. The physical properties are measured in the direction of the mechanism and The tensile test in the tangential direction was performed on 8.3 deg D 882. The final tensile strength and elongation and toughness were determined by this test. The sample was pulled at a rate of 20”/min on a 5 Instron 5500-R. The 1% secant modulus and 2% secant modulus of the direction and transverse direction are performed in accordance with ASTM D 882. The sample is pulled at a rate of 〇5, /min on an lnstr〇n 5500-R. Thickness using Thwing-Albert equipment The company's electronic thickness gauge tester 10 measures an average of 1 point along the thickness of the sheet. Elmendorf tears in the direction of the mechanism and transverse direction are performed according to ASTM D 1922. On the Istron-5500R on a 1 inch sample The pu (polyurethane) foam was subjected to a 180 degree peel test and the peel strength and failure mode were recorded. 15 In addition, the test using "DOW GREAT STUFF" foam was also carried out. The "2" diameter disc of the film was adhered to a 1 cm diameter edge with a small rectangular tape tongue to cure overnight. This sample was hand-drawn with the tape tongue and recorded the adhesion or failure of the foam. The pure polyolefin sample of the group showed no foam adhesion or residue. The film properties are shown in Table 20 below. 204 200911847 Table 20: Film blowing properties 38 39 40 41 42 43 44 45 Thickness (mil) 2.54 4.16 3.37 2.53 3 2.99 3.09 3.34 Standard deviation (mil) 0.09 0.67 0.2 0.14 0.97 0.23 0.17 0.57 1% secant modulus md (〇si) 5570 4256 9236 7741 7694 4340 2445 5347 Standard deviation (psi) 642.8 573.4 614.8 1359.9 1190.6 1797.8 655.7 782.9 2% secant modulus MD(psi) 4044 3506 7472 5656 5423 3656 2689 4632 Standard deviation (psi) 415.3 390.6 324.7 728.8 664.4 813.2 359.5 495 1% secant modulus CD (psi) 5781 4389 7592 8447 6151 5418 4970 10370 Standard deviation (psi) 846.7 386.3 497.4 1339.1 1068.8 1185.9 1784.9 3196.4 2% secant mode CD (psi) 4354 3742 6516 6046 4777 4294 4090 6965 Standard deviation (psi) 541.5 237.5 326.2 765.2 529.9 559.7 894.1 1471.9 Peel strength of the foam (lbf/in) 0.94 0.88 1.04 0.88 0.84 0.87 0.95 1.1 Standard deviation (lbf/ In) 0.06 0.13 0.04 0.03 0.07 0.05 0.01 0.03 Adhesive failure Foam rupture Foam rupture Foam rupture Foam rupture Foam rupture Foam rupture Foam Rupture foam fracture Elmendorf tear MD (g/mil) 158 185 113 144 130 140 159 122 standard deviation 18 12 8 22 18 16 11 11 Elmendorf tear CD (R/mil) 259 200 135 265 254 239 201 232 standard Deviation 39 21 12 10 13 29 20 21 Fracture stress MD (psi) 1767 1467 1575 4020 3957 3718 3631 2093 Standard deviation 183.93 74.9 152.79 401.87 341.55 385.11 372.66 149.92 Fracture strain MD (%) 373 377 330 679 677 696 728 657 Standard deviation 22.05 16.18 17.55 38.44 29.18 38.59 8.83 22.75 Wei edge MD 3573 3276 3404 10433 10630 10099 10244 5694 Standard deviation 493 223 412 1145 1166 1228 893 520 Fracture stress CD (psi) 993 1232 1088 2902 1838 2095 2147 3708 Standard deviation 126.27 136.65 123.84 489.93 134.56 198.98 441.73 383.85 Fracture strain CD (%) 333 388 256 573 612 657 688 710 Standard deviation 28.36 34.96 17.68 132.08 15.56 15.33 67.7 16.68 Toughness CD 2002 2815 2158 5230 4928 5933 6263 10417 Standard deviation 260 409 354 1625 316 559 1365 1207 205 200911847 Samples containing partial LDPE have better tensile properties and toughness in the MD and CD directions. degree. The comparative example of high melt strength ENR 7086 has a higher 1% secant modulus, which implies a lower flexibility than the OBC sample. In some applications, such as footwear, the films of the present invention can be used as a non-LDPE bonded film. This LDPE aids in the treatment by improving the melt strength, but is not an essential component of the film of the present invention. Foam failure bonding occurred in the "DOW GREAT STUFF" foam test and the aforementioned 180 peel test. The film of the present invention can be used in a variety of applications including, but not limited to, adhesive films such as head restraints in automotive articles; adhesive films for footwear components; and any bonding that provides adhesion to polyolefin substrates and polar materials. Membrane, such as in PUS foam, glue and coating. Applications include head coverings, flooring applications, such as barrier films between fabrics and PU foams. The film of the present invention can also be used for a noise vibration pad. The film of the present invention can also be used in applications requiring improved air permeability and higher moisture penetration. The aqueous dispersion aqueous dispersion can be prepared by melt blending a composition of the invention as described herein and water in an extruder to produce a stable, uniform dispersion having an average particle size of substantially 300 nm. . The solids 20 content of the dispersion is substantially from 35 to 50% by weight based on the total weight of the dispersion. Adding a dispersant, for example, 111^1 (:1〇1^350 acid (6% by weight of solids; - synthesizing hydrazine 26, slow acid conversion to potassium salt, available from Baker Petroolite) to the dispersion. This dispersion is then The cast film is applied to a biaxially oriented polypropylene (Bopp) film and the surface energy is measured. 206 200911847 Adhesion Promoter The composition of the invention as described herein, whether pure or as a blend, can be used as a single For the polyurethane adhesion promoter, artificial turf (or artificial grass yarn) is provided by extrusion. 5 For example, one of the compositions of the present invention can be extruded on a tape extrusion line and stretched 5 times. The bundles of 5 can be bundled and stacked on each other, and after the tufts are formed, the artificial turf bundles are simulated. The bundle can be placed in a mold and a polycondensed diol can be injected into one end of the bundle in the mold. _ Isocyanate blend, as shown in Table 21 below. At 25. (After aging for about 30 minutes, a sample of this 10 polymer was used to evaluate the adhesion of the polyurethane. Table 21: Glycol Formulation

Voranol EP 1900 90 pbw 1,4 BD 10 pbw Sylosiv P3 5 pbw DABCO 33 LV 0.2 pbw Isocyanate Isonate M143 Proportion 40 : 100

Therefore, the composition of the present invention can be used as a adhesion promoter for polyurethane in artificial turf and other applications and its reactivity is incorporated into polyolefins, which are used to manufacture artificial turf for improvement. Yarn bundle of artificial turf carpet 15. The adhesion is promoted via a functional group reaction to the application of the polymeric mixture to the carpet-lined polyurethane coating. On the lining side of the carpet, the bundled artificial grass yarn/belt surface is exposed and the coating applied thereto. The adhesion promoter concentration can be 100% of the composition of the invention and can be extended in a blend of polyethylene or propylene which is considered suitable for 20 applications for artificial grass yarns. As low as 10%. One of the compositions of the present invention can also be used in the manufacture of hydrophilic artificial yarns for the purpose of producing "more friendly, surface properties. In particular, thermoplastic polyurethanes and polyethylenes compatible with the present invention can be used. Blends to form a human turf. Although the invention has been described in considerable detail in the foregoing embodiments, the detailed description is intended to be illustrative and not restrictive. The patents, the approved U.S. Patent Application, or the entire disclosure of U.S. Patent Application Serial No. Copolymer (polymer of the invention) and comparative compound (traditional random and ziegler_Natta) melting point as a function of degree and degree. Figure 2 illustrates the thermal melting of several polymers "DSC Tm _ Crystaf 15 Tc" Figure 3. Figure 3 illustrates the effect of an unoriented film made from a specific dilute hydrocarbon multi-block heteropolymer and several conventional random copolymers on the elastic recovery density. Figure 4 illustrates several Rule B /! _ octene copolymer and multi-block ethylene / 1-octene copolymer comonomer content relative to TREF elution temperature. 2 〇帛 5 diagram does not illustrate the multi-segment copolymer (Example 5) and - Comparing the TREF curve and comonomer content of the copolymer (Example F*). Figure 6 illustrates the storage modulus of several multi-block copolymers (polymers of the invention) and comparative examples of random copolymers. A function of temperature. Figure 7 illustrates the TMA (thermomechanical analysis) of a multi-block copolymer (polymer of the invention) and certain ratios 208 200911847 compared to the examples (VersifyTM, ethylene/styrene, AffinityTM) Data and flexible modulus data. [Main component symbol description] (none) 209

Claims (1)

200911847 X. Patent Application Range: ^—A composition comprising at least the following: A) an olefin multi-block heteropolymer; B) a functionalized olefin polymer; and C) a thermoplastic polyamine decanoic acid ester. 2) The composition of claim 1, wherein the olefin multi-block heteropolymer is an ethylene/α·olefin multi-block heteropolymer having at least one of the following characteristics: (1) an average block index Greater than 〇 and up to about 1 〇 and a molecular weight distribution Mw / Mn of greater than about 1.3; (2) at least one molecular component, when eluted between 40 C and 130 ° C when using TREF component, Characterizing that the component has a block index of at least 〇5 and up to about 1; (3) having a Mw/Mn of from about 1.7 to about 3.5, a melting point Tm' of at least one degree Celsius, and a density d of g/cm3, Wherein the values of Tm and d correspond to the following relationship: Tm > -2002.9 + 4538.5(d) - 2422.2(d)2, or (4) a Mw/Mn of from about 1.7 to about 3.5, and characterized by heat of fusion The ΔΗ ' of J/g and one is Celsius, which is defined as the temperature difference between the highest DSC peak and the highest CRYSTAF peak, where the value of at and Newton has the following relationship: For ΔΗ greater than 0 and as high as no j/g, ΑΤ>-0·1299(ΔΗ)+ 62.81, for ΔΗ greater than 130 J/g, AT248°C 210 200911847 where CRYSTAF peak is used until 5 percent polymer accumulation measurement 'and if less than 5 percent of the polymer has an identifiable CRYSTAF peak, then the CRYSTAF temperature is 3 〇 ° C; (5) - elastic recovery Re, whereby ethylene / alpha olefin heterogeneous copolymerization The percentage of the compression molded film of the article measured at 300% strain and 1 cycle, and the density d of g/cm3, wherein when the ethylene/α-olefin heteropolymer is substantially non-crosslinked, Re and d The values satisfy the following relationship: Re >1481-1629(d); (6) - a molecular component which is characterized by the elution between 40 ° C and 130 ° C when TREF is used. Having a molar comonomer content that is at least 5 percent greater than the comparable random ethylene heterogeneous copolymer component eluted at the same temperature, wherein the comparable random ethylene heterogeneous copolymer has the same comonomer and has a The melt index, density and molar comonomer content (based on total polymer) are within 10% of the ethylene Ζα-dilute hydrocarbon heteropolymer; or (7) storage modulus at 25 ° C, G, (25 °C), and at 10 (TC storage modulus 'G' (100 °C) 'where G (25 ° C) to G, (100 ° C) ratio between about 1:1 to about 9: 1. 3. The composition of claim 1 or 2, wherein the olefin multi-block heterogeneous The copolymer is an ethylene/α-olefin multi-block heteropolymer having a density of from 0.85 g/cc to 0.93 g/cc. 4. The composition of any of the preceding claims, wherein the thermoplastic polyurethane comprises a chemical unit derived from (1) at least one polyester and (2) at least one aromatic or aliphatic diisocyanate. 211 200911847 5. 6. 7. 8. 9. 10. 11. 12. 13. 14. For the composition of the patent application 4:1 § § ^ ^, wherein the polyester chemical unit is formed from caprolactone . The composition of claim 4, wherein the thermoplastic polyurethane comprises ruthenium, .1 and ruthenium, and 3-bis(isocyanomethyl)cyclohexane And a chemical unit derived from a mixture of bis(isocyanohydrazide)5 hexane. A composition according to any one of the preceding claims, wherein the thermoplastic polyamino group is a monomer unit comprising a polyether. A composition according to any one of the preceding claims, wherein the thermoplastic polyurethane is 密度__.9Gg/ee to a density of 13_. For example, if you apply for a supplement, “Purchasing — “The thermoplastic polyurethane has a smelting index from M g/lG min to · g/lG minutes (12). The composition of any of the preceding claims, wherein the functionalized olefin-based polymer has a density of from 0.84 g/cc to 〇.93 g/cc. The composition of any of the preceding claims, wherein the medium functionalized dilute (tetra) polymer has a melting index (12) from G 2 g/l G minutes to 1 GG g/l G minutes. The composition of any of the preceding claims, wherein the functionalized polymer is a functionalized ethylene & olefin heteropolymer, and wherein the alpha flue is selected from the group consisting of 1-propene and 1-butyl Alkene, 1-hexene and 1·octane. A composition according to any one of the preceding claims, wherein the functionalized ene-based polymer is a functionalized propylene/ethylene heteropolymer. The composition of any of the preceding claims, wherein the functionalized olefinic polymer comprises at least one of the following functional groups covalently bonded to the olefinic polymer 212 200911847: N-RrNHR2 Λ 5 wherein R is a divalent hydrocarbon group, and R2 is a monovalent hydrocarbon group containing at least 2 carbon atoms, and is optionally substituted with a hetero atom-containing group. The composition of any one of claims 1 to 13, wherein the functionalized olefin-based polymer comprises at least one of the following functional groups covalently bonded to the olefin-based polymer chain: 〇 N-RrOH Η ο · wherein & is a divalent hydrocarbon group. The composition of any one of claims 1 to 13, wherein the functionalized olefin-based polymer comprises at least one of the following functional groups covalently bonded to the olefin polymer chain: Ri \ r2 wherein R1 and R2 are each independently hydrogen or a C1-C20 hydrocarbyl group, which is a line 213 200911847 or a branch; R4 is a divalent hydrocarbon group which is linear or branched; X is OH or NHR5, wherein R5 is one A hydrocarbyl group which is linear or branched, or a monohydroxyethyl group. 17. The composition of any one of claims 1 to 13, wherein the functionalized olefin-based polymer comprises (1) an olefin-based polymer and (2) - selected from an anhydride-containing compound, and a rebel A compound of an acid compound or a mixture thereof is formed. 18. The composition of claim 17, wherein the anhydride-containing compound is maleic anhydride. 19. The composition of any of the preceding claims, wherein the functionalized olefin-based polymer is present in an amount less than or equal to 20 weight percent based on the total weight of the composition. 20. The composition of any of the preceding claims, wherein the functionalized olefinic polymer is present in an amount of less than or equal to 10 weight percent based on the total weight of the composition. 21. The composition of any of the preceding claims, further comprising a low density polyethylene (LDPE). The composition of any one of claims 21, wherein the LDPE has a melt index of from 0.2 to 100 g/min (190 ° C / 2.16 kg). 23. An article comprising at least one component formed from the composition of any of the preceding claims. 24. A blown film comprising at least one component formed from the composition of any one of claims 1 to 23. 25. The blown film of claim 24, wherein the film is an adhesive film. 26. The blown film of claim 24 or 25, wherein the film is a component of a car 214 200911847 component. 27. The boasting of claim 24 or 25, wherein the film is a component of a footwear component. 28. The blown film of claim 27, wherein the footwear component is selected from the group consisting of: outsole, midsole, outsole, overmolded article, natural leather Articles, synthetic leather items, a shoe upper, laminate parts, coated articles, boots, shoes, rubber footwear, and the like. 29. The blown film of claim 24, wherein the film is a barrier film. 30. The blown film of claim 29, wherein the barrier film is between a fabric and a polyurethane foam. 31. The blown film of claim 24 or 25, wherein the film is a component of a floor article. 32. An injection molded article' comprising at least one component formed from the composition of any one of claims i to 23. 33. The injection molded article of claim 32, wherein the composition is "blend in a press, the form. 34. The injection molded article of claim 32, wherein the composition is A composition of the compound. 35. An overmolded article comprising at least one component formed from the composition of any one of the above claims. 36. Overmolding as claimed in claim 35 The article, the composition of which is a "blend in a press". 37. The overmolded article of claim 35, wherein the composition is in the form of a compound blend.