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WO2017038855A1 - Élément composite et outil de coupe - Google Patents

Élément composite et outil de coupe Download PDF

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Publication number
WO2017038855A1
WO2017038855A1 PCT/JP2016/075425 JP2016075425W WO2017038855A1 WO 2017038855 A1 WO2017038855 A1 WO 2017038855A1 JP 2016075425 W JP2016075425 W JP 2016075425W WO 2017038855 A1 WO2017038855 A1 WO 2017038855A1
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WIPO (PCT)
Prior art keywords
layer
phase
cemented carbide
based cemented
composite
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2016/075425
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English (en)
Japanese (ja)
Inventor
五十嵐　誠
藤原　和崇
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Mitsubishi Materials Corp
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Mitsubishi Materials Corp
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Publication date
Priority claimed from JP2016165182A external-priority patent/JP6694597B2/ja
Application filed by Mitsubishi Materials Corp filed Critical Mitsubishi Materials Corp
Priority to US15/755,402 priority Critical patent/US10661345B2/en
Publication of WO2017038855A1 publication Critical patent/WO2017038855A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F1/00—Metallic powder; Treatment of metallic powder, e.g. to facilitate working or to improve properties
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • B23B27/18—Cutting tools of which the bits or tips or cutting inserts are of special material with cutting bits or tips or cutting inserts rigidly mounted, e.g. by brazing
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/08—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on tungsten carbide
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
    • B22F7/00—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression
    • B22F7/02—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers
    • B22F7/04—Manufacture of composite layers, workpieces, or articles, comprising metallic powder, by sintering the powder, with or without compacting wherein at least one part is obtained by sintering or compression of composite layers with one or more layers not made from powder, e.g. made from solid metal

Definitions

  • the present invention relates to a composite member and a cutting tool having excellent joint strength at a joint portion, and more particularly, to a composite member obtained by joining a WC-based cemented carbide and a WC-based cemented carbide, and further to a cutting tool comprising the composite member.
  • This application claims priority based on Japanese Patent Application No. 2015-170656 filed in Japan on August 31, 2015 and Japanese Patent Application No. 2016-165182 filed in Japan on August 25, 2016. Is hereby incorporated by reference.
  • WC-based cemented carbide TiCN-based cermet, cBN sintered body, and the like are well known as tool materials.
  • tool materials are not formed from a single material but as a composite member. Has been proposed to form.
  • Patent Document 1 discloses a bonded body in which a cermet sintered body is a first material to be bonded 1 and a cBN sintered body or a diamond sintered body is a second material to be bonded 3. Bonding is performed between the material to be bonded and the second material to be bonded through the bonding material 2 that does not generate a liquid phase at a temperature lower than 1000 ° C., and the bonding is performed by heating while applying pressure at a pressure of 0.1 MPa to 200 MPa. It has been proposed that the joined body obtained by this does not lower the joining strength of the joining layer even if the brazing material becomes a temperature higher than the temperature at which the brazing material generates a liquid phase during cutting. It is said to be suitable as a high-speed cutting tool or a CVD-coated cutting tool.
  • Patent Document 2 discloses a bonded body in which a cemented carbide sintered body is a first material to be bonded 1 and a cBN sintered body is a second material to be bonded 2.
  • the two materials to be joined are joined to each other by at least two surfaces consisting of a back surface and a bottom surface of the second material to be joined, with a joining material 3 containing titanium (Ti),
  • TiN titanium nitride
  • TiN titanium nitride
  • Patent Document 3 discloses a cBN sintered body containing 20 to 100% by mass of cBN, carbides of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo and W, carbonitrides, and their mutual solid solutions.
  • Hard phase composed of at least one selected from the group consisting of: 50 to 97% by mass, and the balance as a main component of at least one selected from the group consisting of Co, Ni and Fe: 3 to
  • a bonding layer is provided between the cBN sintered body and the hard alloy, and the bonding layer is composed of a ceramic phase and a metal phase. It has been proposed to increase the bonding strength of the composite by setting the thickness to 2 to 30 ⁇ m.
  • Japanese Unexamined Patent Publication No. 2009-241236 A) Japanese Unexamined Patent Publication No. 2012-111187 (A) Japanese Unexamined Patent Publication No. 2014-131819 (A)
  • the composite material proposed in Patent Documents 1 to 3 or a cutting tool made of the composite material exhibits a certain level of performance under normal conditions of cutting. For example, a high feed and a high incision in which a high load acts on the cutting edge. Under heavy cutting conditions, it could not be said that the joining strength was still sufficient, and there was a risk of breakage from the joint. Therefore, there is a demand for a composite member having a higher joint strength and a cutting tool made of the same that does not cause breakage from the joint even under heavy cutting conditions in which a high load acts on the cutting edge.
  • the inventors of the present application have prepared a composite member comprising a WC-base cemented carbide and a WC-base cemented carbide and a cutting tool comprising the composite material, for example, A cutting edge portion made of a composite sintered body obtained by bonding a WC-based cemented carbide (backing material) and a WC-based cemented carbide tool base (base metal) simultaneously with sintering of a cBN sintered body during ultra-high pressure and high-temperature sintering.
  • backing material a WC-based cemented carbide
  • base metal base
  • WC-based cemented carbide member A and the other WC-based cemented carbide member (hereinafter referred to as “WC-based cemented carbide member B”) are made of Ti foil.
  • TiC is used as a bonding layer adjacent to the WC-based cemented carbide member A in a composite member in which the WC-based cemented carbide member A and the WC-based cemented carbide member B are bonded by a bonding layer.
  • a first A layer composed of a phase and a metal W phase is formed; a second A layer composed of a TiCo phase and a metal Ti phase is formed adjacent to the first A layer; and the WC-based cemented carbide member B Similarly, a 1B layer composed of a TiC phase and a metal W phase is formed as a bonding layer adjacent to the WC-based cemented carbide member B, and also composed of a TiCo phase and a metal Ti phase adjacent to the 1B layer.
  • a second B layer is formed and further sandwiched between the second A layer and the second B layer.
  • the WC-based cemented carbide member A the first A layer—the second A layer—the remaining Ti layer—the second B layer—the first B layer—the WC-based cemented carbide member.
  • the area ratio and the layer thickness of the TiC phase in the first A layer and the first B layer, and the area ratio and the layer thickness of the TiCo phase in the second A layer and the second B layer are within an appropriate range.
  • the adhesion strength and bonding strength between the WC-based cemented carbide member and the bonding layer can be improved.
  • the TiC phase in the first B layer By sequentially increasing the area ratio from the WC-based cemented carbide member B side toward the second B-layer side, the adhesion strength and bonding strength between the WC-based cemented carbide member and the joining layer can be further improved. I found out.
  • a composite member in which one WC-based cemented carbide member A and the other WC-based cemented carbide member B are joined via a joining layer (A) A first A layer composed of a TiC phase and a metal W phase is formed adjacent to one WC-based cemented carbide member A, and the average area ratio of the TiC phase in the first A layer is 40 to 60%. And the thickness of the first A layer is 0.5 to 3 ⁇ m, (B) A second A layer composed of a TiCo phase and a metallic Ti phase is formed adjacent to the 1A layer, and the average area ratio of the TiCo phase in the second A layer is 50 to 95%.
  • the thickness of the 2A layer is 0.5-3 ⁇ m
  • (C) A first B layer composed of a TiC phase and a metal W phase is formed adjacent to the other WC-based cemented carbide member B, and the average area ratio of the TiC phase in the first B layer is 40 to 60%. And the thickness of the first B layer is 0.5 to 3 ⁇ m
  • (D) A second B layer composed of a TiCo phase and a metallic Ti phase is formed adjacent to the 1B layer, and the average area ratio of the TiCo phase in the second B layer is 50 to 95%.
  • the thickness of the 2B layer is 0.5-3 ⁇ m
  • the area ratio of the metal W phase in the first A layer gradually decreases from one WC-based cemented carbide member A side toward the second A layer side, or occupies the first B layer.
  • a cutting tool comprising the composite member according to any one of (1) to (3).
  • a joining member (3) is disposed between one WC-based cemented carbide member A (1) and the other WC-based cemented carbide member B (2) (FIG. 1 (a)).
  • Reference one WC-based cemented carbide member A (1) and the other WC-based cemented carbide member B (2) are abutted with each other via the joining member (3), and a predetermined pressure is applied.
  • the WC-based cemented carbide member (1) is joined to the joining member (3) by solid phase diffusion bonding over a predetermined temperature and time (see FIG. 1B).
  • a composite member (6) according to one embodiment of the present invention in which the members are bonded to each other via a bonding layer (7) (hereinafter referred to as "the composite member of the present invention") can be produced (Fig. 1 (c)).
  • FIG. 2 shows an enlarged schematic view of FIG. 1 (c).
  • a first A layer (8) is formed adjacent to one WC-based cemented carbide member A (1).
  • a second A layer (9) is formed adjacent to the layer (8).
  • a first B layer (12) is formed adjacent to the other WC-based cemented carbide member B (2), and a second B layer (11) is formed adjacent to the first B layer (12).
  • a residual Ti layer (10) exists in the central region of the bonding layer (7) sandwiched between the second A layer (9) and the second B layer (11).
  • One WC-based cemented carbide member A (1) the first A layer (8) —the second A layer (9) —the remaining Ti layer (10) —the second B layer (11) —the first B layer (12) —
  • the composite member (6) joined in the order of the other WC-based cemented carbide member B (2) is formed.
  • the joining layer (7) referred to in this specification is the first A formed between the one WC-based cemented carbide member A (1) and the other WC-based cemented carbide member B (2).
  • the whole layer consisting of the layer (8), the second A layer (9), the remaining Ti layer (10), the second B layer (11) and the first B layer (12) is said.
  • the solid phase diffusion bonding in the above-mentioned specification of the present application is the following bonding means. That is, the WC-based cemented carbide member (1) and the WC-based cemented carbide member (2) are brought into contact with each other via the joining member (3), and are maintained at a predetermined temperature and time with a predetermined pressure applied. By this, a joining member and a WC group cemented carbide component are made to react and an alloy is formed. Under the present circumstances, it can be set as the joining which was excellent in the intensity
  • the melting point of the bonding member (3) itself is relatively high (1200 ° C or higher). Reacting with the WC-based cemented carbide at 1000 ° C. or less, being able to control the reaction so that the brittle phase produced by the reaction does not reduce the strength of the joint interface, and the WC-based cemented carbide (1, 2)
  • the mutual diffusion of the joining member (3) conditions such as the difficulty of generating Kirkendall voids caused by an unbalanced diffusion rate are required.
  • Ti foil was used as a joining member (3) meeting such a requirement.
  • the finally formed composite member (6) In the production of the composite member (6) of the present invention, since the WC-based cemented carbide members (1, 2) and the joining member (3) are solid phase diffusion joined, the finally formed composite member (6) In the bonding layer (7), layers having different component compositions, that is, the first A layer (from the one WC-based cemented carbide member A (1) to the other WC-based cemented carbide member B (2) ( 8) The second A layer (9), the remaining Ti layer (10), the second B layer (11), and the first B layer (12) are formed. The first A layer (8) formed adjacent to one WC-based cemented carbide member A (1) and the second layer formed adjacent to the other WC-based cemented carbide member B (2).
  • the 1B layer (12) (hereinafter, the first A layer and the first B layer may be collectively referred to as “first layer”) is a first layer composed of a TiC phase and a metal W phase.
  • the average area ratio of the TiC phase in the layer is 40 to 60%, and the thickness of the first layer is 0.5 to 3 ⁇ m.
  • a second A layer (9) is adjacent to the first A layer (8), and further a second B layer (11) (hereinafter referred to as a second A layer and a second B layer is adjacent to the first B layer (12).
  • second layer is composed of a TiCo phase and a metallic Ti phase, and the average area ratio of the TiCo phase in the second layer is 50.
  • the thickness of the second layer is 0.5 to 3 ⁇ m.
  • the metal W phase in the first layer has a thermal expansion coefficient smaller than that of the WC-based cemented carbide
  • the TiC phase has a thermal expansion coefficient larger than that of the WC-based cemented carbide but smaller than that of the metal Ti. Therefore, the apparent thermal expansion coefficient of the first layer is an intermediate value between the WC-based cemented carbide and the metal Ti. Therefore, by forming the first layer composed of the TiC phase and the metal W phase in contact with the WC-based cemented carbide, the WC-based cemented carbide (1, 2) and the bonding layer (7) are caused by the difference in thermal expansion coefficient. The thermal stress at the time of bonding generated between the two is relaxed, and the formation of residual stress is also suppressed.
  • the average area ratio of the TiC phase in the first layer is set to 40 to 60%. This is because when the average area ratio of the TiC phase is less than 40% or exceeds 60%, the first layer cannot sufficiently perform the stress relaxation function. Further, if the thickness of the first layer is less than 0.5 ⁇ m, sufficient stress relaxation cannot be achieved. On the other hand, if the layer thickness exceeds 3 ⁇ m, the brittleness of the first layer becomes obvious, and the composite member (6) When a high load is applied to the bonding layer (7), cracks are likely to be generated and a crack propagation path is formed, and it becomes impossible to maintain a strong bonding state with the WC-based cemented carbide. Is 0.5 to 3 ⁇ m.
  • the average area ratio of the TiC phase in the first layer is 40 to 60%, but within the range of the average area ratio 40 to 60% of the TiC phase, the WC-based cemented carbide side
  • the WC-based cemented carbide Since the thermal expansion coefficient sequentially increases from the side toward the second layer (or the remaining Ti layer), a relatively smooth change in the thermal expansion coefficient is formed in the first layer.
  • the occupied area ratio of the metal W phase on the WC-based cemented carbide side is relatively increased, and the occupied area ratio of the metal W phase is sequentially increased toward the second layer (or remaining Ti layer) side. It is desirable to reduce it.
  • the effect of reducing the residual stress is effective even with either the first A layer (8) or the second B layer (11), but both the first A layer (8) and the second B layer (11) are effective.
  • the occupied area ratio of the metal W phase on the WC-based cemented carbide side is relatively increased, and the occupied area ratio of the metal W phase is sequentially increased toward the second layer (or remaining Ti layer) side. Since the effect of reducing the residual stress is further increased by reducing the thickness, it is desirable to form the above structure in both the first A layer (8) and the second B layer (11).
  • a layer composed of a TiCo phase and a metallic Ti phase is formed as the second layer in the bonding layer (7), but the formation of the TiCo phase prevents the precipitation of the metallic Co phase having a large thermal expansion coefficient.
  • the stress relaxation is achieved, and the presence of the metallic Ti phase relaxes the difference in thermal expansion coefficient between the first layer and the remaining Ti layer (10) located substantially in the center of the bonding layer (7). Demonstrate.
  • the average area ratio of the TiCo phase in the second layer is less than 50%, precipitation of metal Co cannot be avoided, and local thermal stress is generated by the metal Co present in the second layer, It tends to be a separation starting point in the second layer.
  • the average area ratio of the TiCo phase in the second layer exceeds 95%, the thermal stress relaxation effect between the first layer and the remaining Ti phase (10) is not sufficiently exhibited. Therefore, the average area ratio of the TiCo phase in the second layer is 50 to 95%. If the thickness of the second layer is less than 0.5 ⁇ m, sufficient stress relaxation cannot be achieved. On the other hand, if the thickness of the second layer exceeds 3 ⁇ m, the brittleness of the second layer becomes obvious and the composite member (6) When a high load is applied to the bonding layer (7), cracks are likely to be generated and a crack propagation path is formed, and a strong bonding state with the WC-based cemented carbide cannot be maintained. Is 0.5 to 3 ⁇ m.
  • An unreacted residual Ti layer (10) in the solid phase diffusion bonding is formed in the middle of the bonding layer (7), that is, between the second A layer (9) and the second B layer (11).
  • the first layer and the second layer having the stress relaxation action of the bonding layer (7) are each formed with a thickness of 0.5 to 3 ⁇ m, but the solid phase diffusion bonding conditions are within an appropriate range.
  • Exceeding the above the formation reaction of the TiC phase of the first layer or the TiCo phase of the second layer is excessively promoted, and the residual Ti layer (10) disappears. As a result, the layer becomes brittle and locally The generation of thermal stress causes the strength of the bonding layer (7) to decrease.
  • a Ti foil having a thickness of 4 to 50 ⁇ m can be used as the bonding member (3).
  • the layer thickness of the remaining Ti layer (10) is desirably 2 to 40 ⁇ m.
  • the composite member (6) of the present invention can be produced, for example, by the following method. First, a pretreatment for introducing a strain into the joint surface by blasting each joint surface of one WC-base cemented carbide member A (1) and the other WC-base cemented carbide member B (2). Do. Next, a Ti foil as a joining member (3) is sandwiched between one WC-based cemented carbide member A (1) and the other WC-based cemented carbide member B (2). By holding at a predetermined temperature of 600 to 900 ° C.
  • the strain of WC and Co is alleviated at the time of joining, and at the same time, This reaction is promoted and a uniform reaction is realized even under a relatively low temperature condition of 600 to 900 ° C., and a first layer composed of a TiC phase and a metal W phase and a second layer composed of a TiCo phase and a metal Ti phase are provided in a predetermined A remaining Ti layer (10) is formed in the middle of the bonding layer (7) sandwiched between the second A layer (9) and the second B layer (11).
  • one WC-based cemented carbide member A (1) is used as the cutting edge portion side, and the other WC-based cemented carbide member B (2) is used as a tool base.
  • a cutting tool can be constructed. That is, one WC-based cemented carbide member A (1) of the composite member (6) is used as the backing material of the cBN sintered body on the cutting edge side, and the other WC-based cemented carbide member B (2) is used.
  • a tool base base metal
  • a cBN cutting tool can be formed.
  • the bonding layer is observed in a longitudinal section using a scanning electron microscope and an energy dispersive X-ray spectrometer, and a WC-based cemented carbide member ( 1, 2) and the interface between the bonding layers, element mapping is performed within a range of ⁇ 100 ⁇ m in a direction perpendicular to the interface.
  • the location of each of WC, Co, metal W, TiC, metal Ti, and TiCo is specified, the location where WC and Co are present is the cemented carbide member, and the location where metal W and TiC are present
  • One layer is a second layer where metal Ti and TiCo exist, and a remaining Ti layer where metal Ti is mainly present.
  • Ten straight lines perpendicular to the abutting surfaces of the WC-based cemented carbide members (1, 2) are drawn at intervals of 1 ⁇ m or more, and the distance of these straight lines crossing each layer is averaged to obtain the thickness of each layer.
  • the first layer and the second layer were separated and extracted from the mapping result by image processing, and the area ratio occupied by the TiC phase in the first layer and the area ratio occupied by the TiCo phase in the second layer were determined. Moreover, the change of the area ratio of the metal W phase in a 1st layer can be calculated
  • the present invention is a composite member in which one WC-based cemented carbide member A and the other WC-based cemented carbide member B are joined through a joining layer formed by solid phase diffusion joining using a Ti foil as a joining member.
  • the bonding layer includes a first layer composed of a TiC phase and a metal W phase, a second layer composed of a TiCo phase and a metal Ti phase, and a residual Ti layer, and specifies a phase formed in each layer. Since the internal residual stress is made as small as possible by controlling the thermal expansion coefficient over the entire composite member, between one WC-based cemented carbide member A-bonding layer-the other WC-based cemented carbide member B. It has excellent bonding strength.
  • the strength of the composite member as a whole is improved, and even when a high load is applied to the composite member, no breakage occurs in the bonding layer portion. Therefore, the cutting tool composed of the composite member does not cause breakage from the joining layer portion even when subjected to heavy cutting where a high load acts on the cutting edge. It exhibits excellent cutting performance.
  • FIG.1 Schematic diagram (image used for elemental mapping of longitudinal section) of WC-based cemented carbide member-first layer-second layer-remaining Ti layer of the composite member of the present invention is shown.
  • the black portion and the white portion in the first layer correspond to TiC and metal W, respectively.
  • the light gray part and the dark gray part correspond to TiCo and metal Ti, respectively.
  • the W content is large on the upper layer side, and the W content decreases toward the lower layer side.
  • WC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder and Co powder each having an average particle diameter of 0.5 to 1 ⁇ m were prepared. These raw material powders are shown in Table 1. It is blended into the blended composition, wet mixed in a ball mill for 24 hours, dried, and then pressed into a green compact at a pressure of 100 MPa, and this green compact is vacuumed at 6 Pa, temperature 1400 ° C., holding time 1 hour. Sintering was performed under the conditions to form four types of WC-based cemented carbide sintered bodies (hereinafter simply referred to as “superhard alloys”) A-1 to A-4 shown in Table 1.
  • superhard alloys WC-based cemented carbide sintered bodies
  • cBN powder, TiN powder, TiCN powder, TiB 2 powder, TiC powder, AlN powder, and Al 2 O each having an average particle size in the range of 0.5 to 4 ⁇ m are used as raw material powders for the cBN sintered body.
  • 3 powders were prepared, these raw material powders were blended in a prescribed composition, wet mixed with acetone for 24 hours in a ball mill, dried, and then pressure having a size of 15 mm diameter ⁇ 1 mm thickness at 100 MPa pressure. Press-molded into powder.
  • the cemented carbides A-1 to A-4 are formed into a sintered body having a diameter of 15 mm ⁇ thickness of 2 mm, and this is used as a backing material during the sintering of the cBN sintered body.
  • cBN compacts were laminated in the combinations shown in Table 2, and this laminate was then sintered using an ultrahigh pressure generator at a temperature of 1300 ° C., a pressure of 5.5 GPa, and a time of 30 minutes.
  • Composite sintered bodies B-1 to B-4 were produced.
  • the area% of cBN was determined as the volume% by image analysis of the SEM observation result of the cross-section polished surface of the cBN sintered body.
  • the joining members shown in Table 3 are inserted between the cemented carbides A-1 to A-4 and the composite sintered bodies B-1 to B-4, and the conditions shown in Table 4, ie, 1 to 1 Using a 50 ⁇ m thick Ti foil as the joining member, hold it at a predetermined temperature in the range of 600 to 900 ° C. for 5 to 600 minutes in a vacuum of 1 ⁇ 10 ⁇ 3 Pa or less, and apply a pressure of 0.5 to 10 MPa.
  • the composite sintered body and the cemented carbide were pressure bonded under the conditions described above to produce the composite members 1 to 9 of the present invention shown in Table 6.
  • the composite sintered body is such that the cBN sintered body is the outer surface and the backing material is the inner surface, that is, the WC-based cemented carbide that is the backing material and the WC-based cemented carbide that is the tool base (base metal) are the bonding members. It arrange
  • a joining member having the size shown in Table 3 was used, and this was interposed between cemented carbides A-1 to A-4 and composite sintered bodies B-1 to B-4.
  • the composite sintered body and the cemented carbide were pressure-bonded under the conditions shown in Table 5 to produce comparative example composite members 1 to 10 shown in Table 7.
  • the joint arrangement of the composite sintered body was the same as that of the composite member of the present invention.
  • High temperature shear strength measurement test For the composite members 1 to 9 of the present invention and the comparative composite members 1 to 10 produced as described above, a shear strength measurement test was performed in order to measure the strength of the joint.
  • the test pieces used for the test were composite sintered bodies: 1.5 mm (W) ⁇ 1.5 mm (L) ⁇ 0.00 mm from the composite members 1 to 9 of the present invention and the composite members 1 to 10 of the comparative example prepared above.
  • test piece The upper and lower surfaces of the test piece are clamped and fixed, and a prismatic pressing piece made of cemented carbide with a side of 1.5 mm is used.
  • the ambient temperature is set to 600 ° C., and a load is applied near the center of the upper surface of the test piece. The load at which the test piece breaks was measured. Tables 6 and 7 show the measured shear strength values.
  • FIG. 3 shows a schematic diagram (image used for elemental mapping of the longitudinal section) of the WC-based cemented carbide member-first layer-second layer-residual Ti layer of the composite member of the present invention.
  • the black portion and the white portion in the first layer correspond to TiC and metal W, respectively.
  • the second layer second A layer (9)
  • the light gray part and the dark gray part correspond to TiCo and metal Ti, respectively.
  • the W content is large on the upper layer side, and the W content decreases toward the lower layer side.
  • Element mapping is performed within the range of ⁇ 100 ⁇ m in the direction perpendicular to the interface centering on the interface between the WC-based cemented carbide member and the bonding layer, and the WC phase, Co phase, TiC phase, metal W phase, TiCo phase, and metal Ti While specifying the phase, the cemented carbide member, the first layer, the second layer, and the remaining Ti layer were specified. Moreover, the area ratio which a TiC phase and a TiCo phase occupy was measured from the result of element mapping.
  • the first layer is equally divided into three layers in the thickness direction with the carbide member side layer, the center layer, and the second layer side layer, and the area ratio of the metal W phase in each layer is obtained from the element mapping result. It was. Furthermore, the layer thicknesses of the first layer, the second layer, and the remaining Ti layer were determined. In addition, the center partial area
  • Tables 6 and 8 show the results of the first A layer, the second A layer, the remaining Ti layer, and the shear strength.
  • Tables 7 and 9 show the measurement results of the first B layer and the second B layer.
  • the first A layer and the first B layer, and the second A layer and the second B layer were substantially equivalent. The description of the second B layer was omitted.
  • a cutting tool made of a composite member was produced as follows.
  • the composite sintered bodies B-1 to B-4 produced above were cut into a planar shape: an isosceles triangle having an opening angle of 80 ° with a side of 4 mm ⁇ thickness: 2 mm.
  • the cemented carbides A-1 to A-4 are formed into a sintered body having a planar shape: 12.7 mm inscribed circle and an open angle of 80 ° rhombus ⁇ thickness: 4.76 mm.
  • a notch having a size corresponding to the shape of the composite sintered body was formed in one corner of any one of the upper and lower parallel surfaces of the bonded body using a grinding machine.
  • the area of the bottom surface of this notch is 2.96 mm 2 and the area of the side surface is 4.89 mm 2 .
  • the joining members shown in Table 3 are inserted between the cemented carbides A-1 to A-4 and the composite sintered bodies B-1 to B-4, and the composite sintered body is subjected to the conditions shown in Table 4.
  • the WC base cemented carbide are pressure bonded, and after cutting the outer periphery of this composite member, the cutting edge portion is subjected to a honing process of R: 0.07 mm to have an ISO standard / CNGA120408 insert shape.
  • Tools 1 to 9 were produced.
  • the composite sintered body was arranged so that the cBN sintered body was the outer surface and the backing material was the inner surface, that is, the backing material and the tool base (base metal) were joined via the joining member. Further, it was confirmed that the joint portions of the cutting tools 1 to 9 of the present invention were substantially the same as the composite members 1 to 9 of the present invention shown in Table 6.
  • the composite members 1 to 9 of the present invention have superior joint strength as compared with the comparative composite members 1 to 10. Further, from the results shown in Table 10, the cutting tools 1 to 9 of the present invention composed of the composite members 1 to 9 of the present invention exhibit excellent cutting performance over a long period of use without the removal of the cutting edge. On the other hand, it can be seen that, in the comparative cutting tools 1 to 10 composed of the comparative composite members 1 to 10, the cutting edge falls off from the joint during cutting, and the tool life is reached early.
  • the insert has been specifically described as an example.
  • the present invention is not limited to the insert, and all cutting tools having a joint between the cutting edge portion and the tool body, such as a drill and an end mill. Needless to say, the present invention is applicable to drilling tools such as bits.
  • the composite member of the present invention has a high bonding strength, and the cutting tool produced from this composite member can be used for high-load cutting of various steels and cast irons, and is stable over a long period of time. Since the cutting performance is exhibited, it is possible to satisfactorily cope with high performance of the cutting device, labor saving and energy saving of the cutting work, and further cost reduction.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)

Abstract

L'invention concerne un élément composite (6) permettant de réunir des éléments en carbure cémenté à base de WC (1, 2) entre lesquels est interposée une couche de jonction (7) formée par la jonction par diffusion en phase solide d'un élément de jonction (3) qui comprend une feuille de Ti, et un outil comprenant l'élément composite (6), dans lesquels : la couche de jonction (7) est constituée à partir de premières couches (8, 12) qui sont adjacentes aux éléments en carbure cémenté à base de WC (1, 2) et qui comprennent une phase de W métallique, de telle sorte que la phase de TiC occupe une surface moyenne de 40 à 60 %, des secondes couches (9, 11) qui sont adjacentes aux premières couches (8, 12) et qui comprennent une phase de TiCo et une phase de Ti métallique, de telle sorte que la phase de TiCo occupe une surface moyenne de 50 à 95 %, et une couche de Ti résiduel (10) ; et la surface de la phase de W métallique dans la première couche (8, 12) diminue de préférence graduellement du côté de l'élément en carbure cémenté au côté de la seconde couche.
PCT/JP2016/075425 2015-08-31 2016-08-31 Élément composite et outil de coupe Ceased WO2017038855A1 (fr)

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JP2015-170656 2015-08-31
JP2015170656 2015-08-31
JP2016-165182 2016-08-25
JP2016165182A JP6694597B2 (ja) 2015-08-31 2016-08-25 複合部材及び切削工具

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN111347146A (zh) * 2018-12-24 2020-06-30 核工业西南物理研究院 一种钨与热沉材料连接头及其制备方法
CN111347147A (zh) * 2018-12-24 2020-06-30 核工业西南物理研究院 一种钨与热沉材料的热等静压连接方法
US20220055133A1 (en) * 2017-05-10 2022-02-24 Board Of Trustees Of Michigan State University Brazing methods using porous interlayers and related articles

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04210379A (ja) * 1989-09-14 1992-07-31 De Beers Ind Diamond Div Ltd 複合研摩成形体
JP2007301590A (ja) * 2006-05-10 2007-11-22 Miyagi Prefecture 接合体の製造方法
US20070290545A1 (en) * 2006-06-16 2007-12-20 Hall David R An Attack Tool for Degrading Materials
JP2015142941A (ja) * 2013-12-25 2015-08-06 三菱マテリアル株式会社 接合用ろう材およびそれを用いた複合部材、切削工具

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04210379A (ja) * 1989-09-14 1992-07-31 De Beers Ind Diamond Div Ltd 複合研摩成形体
JP2007301590A (ja) * 2006-05-10 2007-11-22 Miyagi Prefecture 接合体の製造方法
US20070290545A1 (en) * 2006-06-16 2007-12-20 Hall David R An Attack Tool for Degrading Materials
JP2015142941A (ja) * 2013-12-25 2015-08-06 三菱マテリアル株式会社 接合用ろう材およびそれを用いた複合部材、切削工具

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20220055133A1 (en) * 2017-05-10 2022-02-24 Board Of Trustees Of Michigan State University Brazing methods using porous interlayers and related articles
US11724325B2 (en) * 2017-05-10 2023-08-15 Board Of Trustees Of Michigan State University Brazing methods using porous interlayers and related articles
CN111347146A (zh) * 2018-12-24 2020-06-30 核工业西南物理研究院 一种钨与热沉材料连接头及其制备方法
CN111347147A (zh) * 2018-12-24 2020-06-30 核工业西南物理研究院 一种钨与热沉材料的热等静压连接方法
CN111347147B (zh) * 2018-12-24 2022-05-20 核工业西南物理研究院 一种钨与热沉材料的热等静压连接方法

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