[go: up one dir, main page]

WO2012121630A1 - Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau - Google Patents

Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau Download PDF

Info

Publication number
WO2012121630A1
WO2012121630A1 PCT/SE2011/050246 SE2011050246W WO2012121630A1 WO 2012121630 A1 WO2012121630 A1 WO 2012121630A1 SE 2011050246 W SE2011050246 W SE 2011050246W WO 2012121630 A1 WO2012121630 A1 WO 2012121630A1
Authority
WO
WIPO (PCT)
Prior art keywords
roll
less
ingot
weight
terms
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/SE2011/050246
Other languages
English (en)
Inventor
Claude Gaspard
Catherine Vergne
Daniel Batazzi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Akers AB
Original Assignee
Akers AB
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Application filed by Akers AB filed Critical Akers AB
Priority to RU2013142706/02A priority Critical patent/RU2572269C2/ru
Priority to CA2828894A priority patent/CA2828894C/fr
Priority to CN201180000136.7A priority patent/CN103108975B/zh
Priority to PCT/SE2011/050246 priority patent/WO2012121630A1/fr
Priority to AU2011361937A priority patent/AU2011361937B2/en
Publication of WO2012121630A1 publication Critical patent/WO2012121630A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C21D1/25—Hardening, combined with annealing between 300 degrees Celsius and 600 degrees Celsius, i.e. heat refining ("Vergüten")
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
    • B21K1/00—Making machine elements
    • B21K1/02—Making machine elements balls, rolls, or rollers, e.g. for bearings
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/06—Surface hardening
    • C21D1/09—Surface hardening by direct application of electrical or wave energy; by particle radiation
    • C21D1/10—Surface hardening by direct application of electrical or wave energy; by particle radiation by electric induction
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/0068—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for particular articles not mentioned below
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/38—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for roll bodies
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/008—Martensite
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Definitions

  • This invention relates in general to the field of forged rolls and to production of forged rolls. More particularly the present invention relates to forged rolls meeting the requirements of and mainly being directed for use in the cold rolling industry.
  • chrome plating of such rolls is applied to improve the wear resistance in terms of surface texture retention which, in turn, will ensure, for instance, consistent and higher gloss of car bodies after painting.
  • Hard electrolytic deposit techniques as chrome plating were initially developed for temper/skin pass mill applications. In these applications, chrome plated work rolls exhibit 2 to 8 times longer lifetimes than uncoated rolls, mainly because of a better roughness retention. The implementation of this technique was progressively extended to the reduction mills.
  • HSS high speed steel
  • Rolls produced to be used within the cold rolling industry has to manage the processing conditions or the specific operating stresses during usage without getting cracks or be prone to explode. Explosion of a roll can involve safety of operating persons and collateral damage in the mill. Therefore there is a need for a roll with low residual internal stresses.
  • JP09003603 JP53077821, JP57047849, , JP2002285284, JP2002285285, JP10317102, JP1208437, EP0395477 and JP08158018 which describe work rolls for cold rolling to enhance wear and spalling resistance.
  • the general object of the invention is to provide a roll and an industrial process for producing such a roll that is operative during the conditions in a cold rolling mill, preferably in a non- coated form.
  • a more specific object is to provide such a roll and process for producing such a roll while keeping tribological properties such as low friction coefficient, high roughness retention, no dust pollution by iron fines at least equivalent to prior art coated rolls and which exhibit improved mill performances in terms of higher crack resistance and higher safety in operation compared to known rolls. Partial problems
  • the invention further seeks to solve the partial problems of:
  • the present invention provides a forged roll for use in the cold rolling industry and a method for production of such a roll.
  • the roll is preferably non-coated but may also be coated.
  • a first aspect of the invention relates to a forged roll, comprising a steel composition comprising, in terms of % per weight,
  • the remaining portion of the steel being substantially Fe and possible incidental and/or possibly unavoidable impurities
  • microstructure of the roll comprises:
  • the roll of the invention comprises an open eutectic carbide network delimits a cell-like pattern of eutectic cells.
  • a roll wherein the open eutectic carbide network of said roll comprises dendritic arms.
  • a roll wherein the open eutectic carbide network of said roll is formed as substantially isolated portions of eutectic carbides network.
  • a roll wherein the microstructure of said roll is present at least in the worldng layer of the roll.
  • a roll with a steel composition consisting, in terms of % per weight
  • the roll according to the invention wherein the C content in the steel composition is between 0.8 - 0.99 % C in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the C content in the steel composition is between 0.85 - 0.9 % C in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Mn content in the steel composition is between 0.4 - 0.5 % Mn in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Si content in the steel composition is between 0.85 - 1.15 % Si in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Cr content in the steel composition is between 7.0 - 11 % Cr in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Cr content in the steel composition is between 7.3 - less than ( ⁇ ) 8.0 % Cr in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Mo content in the steel composition is between 1.45 - 1.55 % Mo in terms of % per weight of total roll weight.
  • Ni content in the steel composition is less than ( ⁇ ) 0.3 Ni in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the V content in the steel composition is between 1.3 - 2.1 % V in terms of % per weight of total roll weight.
  • V content in the steel composition is between i.3 - l.6 % V in terms of % per weight of total roll weight.
  • a roll according to the invention further being configured for use as a worldng roll in cold rolling.
  • a roll according to the invention further having a weight of more than 400 kg.
  • a roll according to the invention further having a diameter in the range of 2l5-8oomm.
  • a further aspect of the invention provides a forged roll produced by a process comprising the steps of: a. Providing a steel composition comprising, in terms of % per weight,
  • composition according to the invention is as any of the compositions or combinations of compositions described above.
  • a further aspect of the invention provides a process for manufacturing a non-forged roll according to the invention, the process comprising the steps of: a. Providing a steel composition comprising, in terms of % per weight,
  • the composition according to the invention is as any of the combinations of compositions described above.
  • a process according the invention wherein the ingot is manufactured maintaining a solidification rate higher than 35 °C/min in the working layer or surface of the ingot in the solidification interval.
  • a process according the invention wherein the solidification interval is between 1400-1200°C for said ingot.
  • a process according the invention wherein the ingot is manufactured maintaining a preselected solidification rate in an electro-slag refining furnace (ESR) technique process by controlling the ampere current supply according to a predetermined function of the solidification rate.
  • ESR electro-slag refining furnace
  • a process, wherein the step of forging the ingot to a roll comprises the steps of: a. Heating the ingot to a temperature of about 850 - 1100 °C or between 8oo-iooo°C preferably for a period of about 6 hours; b. Forging the ingot at a temperature above about 800 °C or above 850 °C; c. Repeating steps a-b until the ingot has been formed to a roll that has desired shape and size.
  • a process further, after the forging step, comprising a step of preliminary heat treatment, applied on the roll blank, preferably to a temperature of about 700-iioo°C or between 800 - 900 °C, which may include hydrogen diffusion treatment.
  • a process further comprising a step of superficial hardening by progressive induction heating , preferably at a temperature of about 900-ll50°C.
  • a process wherein the step of tempering the roll comprises the steps of: d. Heating the roll to about 450 - 530 °C or between 450 - 520 °C,
  • a process further comprising machining the roll to texturing a white layer comprising eutectic carbides comprising any of the following optional, individual or combinable aspects regarding the chemical composition or microstructure of the roll mentioned above and further comprising the features of any of the comprising any of the following optional, individual or combinable aspects mentioned below.
  • a further aspect of the invention provides an intermediate product ingot in the production of a roll, the ingot comprising a steel composition comprising, in terms of % per weight,
  • microstructure of the final roll issued from the ingot comprises:
  • a further aspect of the invention provides the use of a forged roll according to the invention for cold rolling material requiring a high rolling load.
  • the roll according to the invention is useful in many applications as a non-coated roll.
  • the roll may also be provided with a coating selected for any current of specific application.
  • the coating may for example be a chromium coating.
  • the roll may also be used in warm rolling applications.
  • Figure 1 shows a schematic picture of a roll according to the invention.
  • Figure 2 shows a schematic view of the roll production process according to the invention.
  • Figure 3 shows a schematic picture of an ingot according to the invention.
  • Figure 4 shows a manufacturing process of an ingot according to the invention.
  • Figure 5 A-B shows a cast microstructure of roll grade made using a production process according to the invention. The roll grade is shown in sectional view of the working layers of the roll grade.
  • Figure 6 A-B shows a cast microstructure of roll grade made using a production process according to the invention.
  • the roll grade is shown in sectional view of the working layers of the roll grade.
  • Figure 7 shows cast microstructure of roll grade made using a production process according to the invention but with the deviation rendered when using too low solidification rate.
  • the roll grade is shown in sectional view of the working layers of the roll grade.
  • Figure 8 shows a first set of examples of solidification rates for roll production process according to the invention.
  • Figure 9 shows a second set of examples of solidification rates for roll production process according to the invention.
  • Figure 10A-B show a cast microstructure of an ingot made in laboratory conditions when using the production process according to the invention.
  • Figure 11 A-B show a cast microstructure of an ingot made in laboratory conditions when using the production process according to the invention but with the deviation rendered when using too high Mo content.
  • Figure 12 shows a schematic view of forging according to the invention.
  • Figure 13 shows a schematic view of the steps of forming the ingot by forging it to a roll according to the invention.
  • Figure 14 shows a schematic view of progressive induction hardening with different frequencies of the roll according to the invention.
  • Figure 15 A-B shows a microstructure of the surface of a roll according to a standard grade after surface texturing (EDT texturing).
  • Figure 15 C-D shows a microstructure of the surface of a roll according to the invention after surface texturing (EDT texturing).
  • Figure 16 A-D shows detrimental defects on a roll generated during manufacturing of rolls with low chromium content and high molybdenum content.
  • Figure 17A shows an embodiment of a microstructure according to the invention with an open eutectic network.
  • Figure 17B shows an example of a microstructure with a closed eutectic network wherein the eutectic carbides 200 form a closed eutectic network with clearly separated eutectic cells 212.
  • Figure 18 shows an example representing the microstructure of a roll surface according to the invention after Electro Discharge Texturing.
  • Figure 19 shows the roll microstructure of a depth of 4mm on the roll surface after tempering and induction hardening of the roll. Detailed description
  • the invention relates generally to a forged roll l which preferably has a weight of more than 400 kg, or, as in embodiments for common applications for example a weight of more than 1000 kg.
  • the roll according to the invention is produced according to a forged roll production method which in its general steps is per se known but is specifically adapted in accordance with the inventive concept to be able to produce a roll according to the invention.
  • the invention is mainly directed to rolls with a weight between 400 kg and 10 000 kg.
  • the roll according to the invention has a diameter 2 of typically more than 200 mm and, for example between 215-800 mm, and a length of the barrel 8 typically between 1-3 meters and a maximum length of typically about 6 meters including the necks 10.
  • the roll 1 has a working layer 4 which corresponds to a part of the outer layer and is typically ranging between 20 mm and 120 mm in diameter, dependent on the application of the specific roll and/ or dependent on the total roll diameter 2.
  • the outer 1/6 part 6 of the diameter 2 of the roll is referred to as the working layer 4 of the roll 1, see figure l.
  • the outer 1/ 6 part 6 of the diameter 2 of the ingot 34 is also referred to as the working layer 4 of the ingot 34 in the text.
  • the roll production process 12 according to the invention is crucial for manufacturing a roll 1 of this size according to the invention.
  • the improved mechanical properties such as low residual internal stresses of the roll of the invention result from the roll production process 12.
  • the microstructure of the roll 1 according to the invention comprises tempered martensite with a retained austenite rate lower than 5% in volume due to the production process of the roll and due to the chemical composition according to the invention.
  • the roll production process according to the invention comprises a selection of the following basic steps schematically shown in the flow diagram of Fig 2: 14. Providing a steel composition
  • the present invention relates to a forged roll (1) produced by a process comprising the steps of: a. Providing a steel composition comprising, in terms of % per weight,
  • the remaining portion of the steel being substantially Fe and possible incidental and/ or possibly unavoidable impurities; b. Manufacturing an ingot maintaining a solidification rate higher than 15 °C/ min in the working layer of the ingot in the solidification interval; c. Forging the ingot to a roll; d. Hardening the roll by induction heating; e. Tempering the roll; thereby achieving a microstructure of the roll (1) that comprises:
  • a process of maldng a forged roll according to the invention comprises the following steps:
  • Step 14 Providing of a steel composition.
  • the steel composition comprises an alloy comprising or consisting of the following constituents indicated in weight % as listed in Table 1.
  • Table 1 the impact of the constituents and the effect of the inventive roll that is achieved by the selected constituents and the specific intervals are explained.
  • any unalloyed steel will contain silicon, manganese, phosphorus and sulphur, which occur unintentionally during manufacture.
  • the addition of further alloying elements to achieve special effects and intentional increase in the manganese and silicon contents results in alloy steel.
  • C content With increasing C content, the strength and harden ability of the steel increase, but its ductility, forgeability, weldability and machinability (using cutting machine tools) are reduced.
  • the level of C is lower than 1% to avoid the formation of too large closed network of eutectic carbides.
  • Mn sulphur to form Mn sulphide, thus reducing the undesirable effect of the iron sulphide.
  • This is of particular importance in free-cutting steel; it reduces the risk of red shortness.
  • Mn very pronouncedly reduces the critical cooling rate, thus increasing hardenability. Yield point and strength are increased by addition of Mn and, in addition, Mn favourably affects forgeability and weldability and pronouncedly increases hardness penetration depth. In the invention Mn is kept lower to 0.5% to avoid excessive brittleness.
  • Si 0.2 -2.0 Silicon is contained in all steel in the same way as manganese, as iron ores incorporate a quantity of it according to their composition. In steel production itself, silicon is absorbed into the melt from the refractory furnace linings. But only those steels are called silicon steels which have Si content of> 0.40%. Si is not a metal, but a metalloid as are also, for example, phosphorus and sulphur. Si deoxidizes. On account of significant reduction of electrical conductivity, coercive field intensity and low wattage loss, Si is used in steels for electrical quality sheet.
  • Iron sulphide leads to red shortness or hot shortness, as the low melting point sulphide eutectics surround the grains in reticular fashion, so that only slight cohesion of the latter occurs and during hot forming the grain boundaries tend to break down. This is further increased by the action of oxygen.
  • As sulphur possesses a considerable affinity for manganese, it is combined in the form of Mn sulphide, as this is the least dangerous of all existing inclusions, being present distributed in point form in the steel. Toughness in transverse direction is reduced significantly by S. To be kept at the lowest level.
  • P ⁇ 0.015 Phosphorus is usually regarded as a steel parasite, as P produces pronounced primary segregation on solidification of the melt and the possibility of secondary segregation in solid state due to the pronounced restriction of the gamma phase.
  • P is to be kept at the lowest level, preferably ⁇ 0.015 W%.
  • Chromium renders steels oil and air-hardenable.
  • Mo 0.6 - 1.6 Molybdenum is usually alloyed together with other elements. Reducing the critical cooling rate improves hardenability. Mo significantly reduces temper brittleness and promotes fine grain formation. Increase in yield point and strength. Pronounced carbide former; cutting properties with high speed steel are improved thereby. Very severe restriction of the gamma phase. Increased high temperature strength. With increased Mo content, forgeability is reduced. Accordingly, its content is maintained under 1,6% to avoid the detrimental formation of ferrite delta.
  • Ni ⁇ 1.0 Nickel in steel produces significant increase in notch toughness, even in the low temperature range, and is therefore alloyed for increasing toughness in case-hardening, heat-treatable and subzero toughness steels.
  • Ni is not carbide former.
  • Pronounced carbide former thus providing level of hardness compatible with cold rolling process, increase in wear resistance, high cutting ability and high temperature strength. It is used therefore primarily as additional alloying element in high speed, hot forming and creep resistant steels. Significant improvement in retention of temper, reduction of overheating sensitivity. V restricts the gamma phase and shifts the Curie point at elevated temperatures.
  • w 0.0 - 2.0 Tungsten is a very pronounced carbide former (its carbides are very hard) and restricts the gamma phase. It improves toughness and prevents grain growth. W increases high temperature strength and retention of temper as well as wear resistance at high temperatures (red heat) and thus cutting ability. It is therefore alloyed primarily to high speed and hot forming tool steels, as well as creep-resistant steel types and to ultrahard steels.
  • Titaniumn account of its very strong affinity for oxygen, nitrogen, sulphur and carbon, Ti has a pronounced deoxidizing, pronounced denitriding and pronounced carbide forming action. Used widely as carbide former. Also possesses grain refining properties. Ti restricts the gamma phase very pronouncedly. In high concentration, it leads to precipitation processes and is added to permanent magnet alloys on account of achieving high coercive field intensity. Ti increases creep rupture strength through formation of special nitrides. Finally, Ti tends pronouncedly to segregation and banding.
  • Niobium (Nb) and Tantalum (Ta) occur almost
  • Zr o.o - 0.5 Zirconium is a carbide former; metallurgical use as alloying element for deoxidation, denitriding and desulphurization, as it leaves minimal deoxidation products behind. Additions of Zr to fully deoxidized sulphur-bearing free-cutting steels have a favourable effect on sulphide formation and thus prevention of red shortness. It increases the life of heating conductor materials and produces restriction of the gamma phase. and further optionally comprising, H2, N2, O2, Al, Cu, each in amounts lower than 0.4 weight %; and wherein the remaining portion of the steel composition is substantially Fe, apart from incidental elements and possibly unavoidable impurities.
  • the steel composition comprises, in terms of % per weight,
  • the remaining portion of the steel is substantially Fe, apart from incidental elements and possibly unavoidable impurities.
  • composition comprises or consists of a combination or a selection of the constituents (weight %) according to the following examples.
  • weight % the constituents (weight %) according to the following examples.
  • the before mentioned embodiment is combined with, substituted by or narrowed by the below variants of constituent amounts.
  • a roll with a steel composition consisting, in terms of % per weight
  • the roll according to the invention wherein the C content in the steel composition is between 0.8 - 0.99 % C in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the C content in the steel composition is between 0.85 - 0.9 % C in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Mn content in the steel composition is between 0.4 - 0.5 % Mn in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Si content in the steel composition is between 0.2 - 1.5 % Si in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Si content in the steel composition is between 0.85 - 1.15 % Si in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Cr content in the steel composition is between 7.0 - 11 % Cr in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the Cr content in the steel composition is between 7.3 - less than ( ⁇ ) 8.0 % Cr in terms of % per weight of total roll weight.
  • Ni content in the steel composition is less than ( ⁇ ) 0.3 Ni in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the V content in the steel composition is between i.3 ⁇ 2.i % V in terms of % per weight of total roll weight.
  • the roll according to the invention wherein the V content in the steel composition is between 1.3 - 1.6 % V in terms of % per weight of total roll weight.
  • Step 16 Manufacturing 16 of a cylindrical shaped ingot 34
  • an intermediate product the ingot 34 produced according to the method of the invention preferably has a diameter 32 of between 450 and 1100 mm, length 30 up to 6 meters and weight between 400 to 30000kg, see figure 3.
  • the method of making an ingot 34 according to the invention involves using a technique which enables fast cooling during the ingot 34 manufacturing.
  • the ingot 34 can be produced using different ingot forming techniques. Suitable manufacturing techniques are those which are capable of being controlled to achieve and maintain a specific minimum solidification rate.
  • the average solidification rate is controlled to be higher than l5°C/min in the surface and preferably also higher than lo°C/min in the core during the formation of the ingot.
  • this solidification rate is maintained while controlling cooling the ingot material in the solidification interval which may for example be between 1400°C to 1200°C.
  • the average solidification rate is controlled to be higher than 35°C /min in the working layer in the solidification interval.
  • Further embodiments of the invention comprise the average solidification rate in the working layer as well as in the core is controlled to be in the range of l5°C/min to 55 °C /min, or alternatively 35 °C /min - 55°C/min, or alternatively 45 °C /min - 55°C/min.
  • solidification parameters in accordance with the invention are for example different types of electro-slag refining furnace (ESR), for example moving mold ESR melting or ESR cladding or spray forming techniques etc.
  • ESR electro-slag refining furnace
  • An ingot made using a solidification rate and a chemical composition as described in any of the above embodiments according to the invention has the following characteristics:
  • an ingot made using a process according to the invention has the following advantages on the rolled product:
  • an electro-slag refining furnace is used for manufacturing of the ingot 34 according to the invention, for a schematic view see figure 4.
  • the electro-slag refining furnace is capable of melting about 300-iiookg/h, and comprises an electrode clamp 36, a stinger 38, an electrode 40, a cooling jacket outlet 42, a cooling jacket inlet 50 for cooling water.
  • the ingot is formed by melting the electrode 40 and thus different layers are formed in the ingot material 48 such as a slag pool 44, which is located near the electrode, and a molten metal pool 46.
  • the ESR also comprises a starting plate 52 which is water cooled 54, see figure 4.
  • the ESR technique may require a starting ingot (electrode 40) obtained by a conventional melting process to be re-melted to form an ingot 48 according to the invention.
  • the re-melting using the ESR is carefully controlled in order to achieve the average solidification rate according to embodiments of the invention, for example an average solidification rate higher than i5°C/min in the working layer and also in the core of the ingot during formation of the ingot.
  • the electrode 40 is in the ESR process thus heated by an electric current, for example a high ampere current to re-melt the steel of the electrode to form an ingot according to the invention.
  • the high ampere current of the electrode 40 is carefully controlled to control the speed of re-melting and this also affects the speed of cooling and thereby the solidification rate.
  • the solidification rate depends on the ampere current fed to the electrode according to a predetermined function. Basically, the higher the ampere current, the higher is the power supplied to re-melt the electrode 40 (see Ohm law). The higher the supplied power, higher is the slag temperature and the lower is the solidification rate.
  • directional solidification can be achieved with a solidification rate according to the invention in the core and in the working layer while cooling the ingot in certain intervals.
  • a solidification rate which in average is higher than i5°C/min both in the core and in the worldng layer of the ingot while cooling the ingot in the solidification interval from 1400°C to
  • the eutectic carbide content in the ingot is held below 5 volume %. This renders a good grindability of the resulting roll.
  • the grindability of the roll is important since during usage of the final roll, grinding is an important procedure to achieve the adequate roughness of the roll regarding cold rolling process. It is known that a concentration of eutectic carbides higher than 5% gives unsatisfactory grindability of such a roll.
  • compositions which comprises high levels of Cr (for example 7-13%). High segregation which is obtained if the solidification rate is too slow defects high chromium ingots.
  • a solidification rate higher than 15 0 C/min during the solidification interval when maldng the ingot gives a low segregation rate resulting in an eutectic carbide content lower than 5% in volume.
  • Example 1 demonstrates the effect the method of the invention has on the microstructure of the roll l according to the invention.
  • Example 2 is a comparative example. The examples are performed during production of roll prototypes in natural scale. The experiments show the important variation of the distribution of eutectic carbides and network shape in the ingot after casting depending on the used solidification rate, see examples l and 2 below and table 2. The distribution of eutectic carbides and network shape which is seen in the ingot is remained in the final roll after forging and tempering according to the invention.
  • This example shows the effect on the microstructure in the roll according to the invention when using a solidification rate higher than i5°C/min during formation of the ingot 34 according to the invention.
  • Figure 5A-B show an example of a microstructure of INGOT 1 according to the invention which is made using a process with a solidification rate in average 50°C/min (on 90mm depth of the ingot) while cooling the ingot from 1400°C to 1200°C.
  • the eutectic cells in the example INGOT 1 according to the invention are small (940, 942), figure 5B shows the fragmented network with to an open eutectic network. See also figure 8 for the different solidification intervals in the different parts of the ingot during the solidification showing the temperature rate in the core 82, the mid-radius 84, 90mm 86, 50mm 88, 30mm 90 and surface 92.
  • Figure 5B is a magnification of figure 5A. See also table 2.
  • Figure 6A-B show an example of a microstructure of INGOT 2 according to the invention which is made using a process with a solidification rate in average i8°C/min (on 90mm depth of the ingot) while cooling the ingot from 1400°C to 1200°C.
  • Figure 6 shows the eutectic cells in the example INGOT 2 according to the invention, and these are small, see for examplecross sectional distance 1024. See also figure 9 for the different solidification intervals in the different parts of the ingot during the solidification 80, showing the temperature rate in the core 100, the mid-radius 102, 90mm 104, 50mm 106, 30mm 108 an surface 110.
  • Figure 6B is a magnification of figure 6A. See also table 2.
  • the method according to the invention ensures absence of segregation in mid-radius of the ingot. Absence of segregation in mid-radius (or 5/6 of inner part of the diameter of the cylindrical roll) guarantees the integrity of the roll during the hardening process.
  • a solidification rate higher than i5°C/min in the working layers thus generates a finer microstructure which, as explained above, is better in terms of grinding and dust pollution, se figures 5A-B and figure 6A-B.
  • This example shows the effect of using a solidification rate lower than i5°C/min during formation of the TEST ⁇ ingot.
  • Figure 7A-C show an example of a microstructure of the TESTi ingot which is made using a process with a solidification rate of lower than 15 (in fact even lower than 10) °C/min while cooling the ingot in the solidification interval from 1400°C to 1200°C.
  • the cells 700 of the comparative TEST 1 ingot in figure 7A-C are larger in size, see for example cross section 708 which has a cross sectional length 708 is larger than the largest cross section in for example of the INGOT 1 in example 1 according to the invention.
  • TEST 1 ingot also shows shrinkage porosities 704.
  • the coarse conglomerate eutectic network 702 can also be seen in figure 7A- C. See also table 2.
  • Figure 7B-C is a magnification of figure 7A.
  • a solidification rate lower than l5°C/min within the solidification interval gives a high
  • a high segregation of the carbides and a coarse carbide network 702 makes a white blank roll or a finished roll made by an ingot according to TEST 1 brittle and thus prone to explode during induction hardening (a white blank roll) or in the cold rolling mill (finished roll).
  • Example 2 also shows that a solidification rate lower than l5°C/min also makes the size of the eutectic cell structure larger and coarser compared to when an ingot is made using
  • a solidification rate higher than i5°C/min during the solidification interval when making the ingot gives a low segregation rate resulting in an eutectic carbide content lower than 5% in volume.
  • Table 2 shows experimental data for test of ingots with different average solidification rate (*) while cooling the ingot from 1400°C to 1200°C on 90mm depth of the ingot
  • Example 3 demonstrate for example the effect the method of the invention and the chemical composition of the ingot has on the microstructure of the ingot and thus also on the roll of the invention.
  • Example 4 is a comparative example.
  • Example 3 and 4 show microstructure of ingots produced by experimentation in the laboratory with controlled solidification device and controlled cooling speeds.
  • This example shows an INGOT 1 microstructure produced according to the method of the invention by experimentation in the laboratory with controlled solidification device and controlled cooling speeds higher than i5°C/min in the solidification interval.
  • an open eutectic carbide system 750 is achieved in the ingot structure, see figure 10A-B. See also table 3.
  • This open eutectic carbide system 750 as is seen in the roll 1 according to the invention is characterized as a dendrite pattern and the eutectic carbide structures 752 is not forming closed eutectic carbides network(as in comparative example 4, TEST2) but instead forms dendrite arms in a network, see figure 10A-B which shows a picture of the microstructure of an ingot with 1.4% Mo is produced according to the process of the invention.
  • This open eutectic carbide system according to the invention makes the roll easier to grind compared to rolls made using higher amounts than 1.6% of Mo.
  • a TEST2 ingot is made using a process of the invention and a composition where the main constituents are according to the above embodiments but with the difference that the chemical composition differs from the invention regarding the amount of Mo.
  • This TEST 2 ingot is produced according to the method of the invention by experimentation in the laboratory with controlled solidification device and controlled cooling speeds higher than l5°C/min in the solidification interval.
  • the amount of Mo is 2.77%, see also table 3.
  • the ingot 34 made according to the previous step of the invention is then forged.
  • the ingot 34 is hot press forged using a a per se known process for simultaneously reducing the cross-sectional area and changing the shape by passing them between a hammer and an anvil forming the ingot to a roll 1 according to the invention.
  • the ingot is heated in a dedicated furnace, see figure 12 for a schematic view of the forging step.
  • the forging step 18 includes the following steps, see figure 12; -Pre-heating 56 of the ingot 34 for about 6h to a temperature of between 8oo-l200°C or between 850-1100 °C.
  • the pre-heating step 56 involves heating the ingot 34 from the surface all the way into the core of the ingot.
  • the temperature during forging is adjusted within the interval 8oo-i200°C or between 850-1100 °C since a higher temperature than 1200°C leads to defects of the ingot structure due to burning of the roll.
  • the reasons for keeping the temperature of the ingot at the indicated temperature interval is that a temperature below 8oo°C leads to crack forming of the ingot. As the ingot 34 cools it becomes stronger and less ductile which may induce cracking if deformation continues.
  • step 60 After preheating (step 56) of the ingot 1, it is forged (step 60) using a forge ratio of 1.35-2.0.
  • the forging step 60 and the preheating step 56 are repeated, this forging cycle commonly being called a heat 58.
  • a heat 58 is repeated as many times as needed to form a roll according to the invention, see figure 12.
  • the roll 1 according to the invention is forged using 3-6 heats 58 to forge the ingot into a roll blank.
  • a roll blank is a roll which has the shape of a roll but still with a barrel that lacks the final treatments to become a roll usable in the mill.
  • the ingot 34 is forged in several heats 58, see figure 13 for a schematic view of forging a roll:
  • Forging a steel composition according to the invention is more difficult to do because of the high alloy content according to the invention than compared to forging example standard steel grades.
  • a roll 1 according to the invention has preferably a diameter 2 between 250-800 mm, see figure 1 and an ingot 34 according to the invention has preferably a diameter 32 between 400-iooomm or between 450-1100 mm.
  • the ingot 34 has the desired eutectic carbide microstructure formed during the manufacturing process of the ingot 34 during the solidification step 80. It is shown that ingots 34 with the eutectic carbide microstructure according to the invention with amounts of eutectic carbides lower than 5 volume % are possible to forge using hot pressure forging techniques. Using an ingot with formed with another process, for example with a solidification rate lower than l5°C/min makes these large rolls to lead to explosion during induction hardening or in the mill.
  • Step 20 Preliminary heat treatment of said roll 1
  • the roll is treated with a preliminary heat treatment step.
  • the roll is heated to between 700 °C - lioo" C during the preliminary heat treatment 20 according to the invention in a furnace and then the roll is kept at that temperature for a certain time until satisfactory hydrogen diffusion has occurred.
  • the preliminary heat treatment normalizing and spheroidal annealing is performed in order to improve machinability of the roll.
  • Step 22 Rough machining 22 of said roll
  • Rough machining 22 of the formed roll 1 according to the invention means removing the outer layer of the forged roll. In one embodiment of the invention of the outer layer is removed during rough machining.
  • the roll is called a black blank before it is treated to rough machining. By removing the oxidation layer on the surface of the roll the black blank roll is then transformed to a white blank.
  • Step 24 Induction hardening of said roll 1
  • the roll is treated by induction hardening.
  • induction hardening of the roll the hard surface of the roll is formed. See figure 14 for a schematic view of the induction hardening step.
  • the roll is slowly moved downwards while an electric current or voltage frequency between 50-ioooHz is applied on through the inductor arrangement 70 during the induction hardening step.
  • the roll 1 is cooled using water cooling 72 after the heating step, see figure 14.
  • the formed hard surface is also called the working layer 4 of the roll and is about 1/6 (see figure 1, number 6) of the total diameter 2 of the roll 1.
  • the roll barrel surface is heated quicldy when lowered through a series of inductors comprising electrical coils leading into a quench box. The fast heat penetration of induction heating and immediate quenching using water produces a defined layer of uniform hardness of the surface of the roll. Both the necks and core of the roll remain at low temperature throughout the process.
  • induction hardening a frequencies typically between 50- 1000Hz are applied on the surface of the roll 1 and a frequency selected from the lower parts of that interval gives deeper working layer 4 of the roll 1. Other factors that affect the depth of the formed working layer are the gap between inductors 70 (if several inductors are used). Also the gap or distance between the inductor 70 and the roll 1 affects the depth of the formed working layer 4.
  • the induction hardening step 24 according to the invention could be of single, double or more frequency/ies.
  • the roll according to the invention explodes using conventional hardening techniques and induction heating is the most suitable technique for hardening of the roll according to the invention. Cooling of the roll 1 during the induction hardening 24 is performed by high flow of cold water.
  • the induction hardening 34 is made by double induction hardening and the cooling of the roll 1 after the induction hardening 24 is made by high flow of water which has a temperature of 40°C and is transported at a flow of about 300 ms/h and the roll is moved downwards at a speed of 0.3mm to 1 mm/s.
  • the induction hardening step 24 takes between 0.5-2I1.
  • the roll 1 is tempered.
  • the purpose of the tempering step is to reduce the brittleness of the roll and to adjust the level of hardness.
  • the tempering step 26 is a crucial step during the formation of the roll because it decreases the internal stresses.
  • the roll achieves its final micro structure by diffusion and secondary precipitation of carbides. Air cooling is applied between the tempering heating steps.
  • the rolls are tempered preferably 3 times at 450-530 °C.
  • the tempering step makes the roll obtain the required hardness level higher than 780 HV or between 780-840 HV.
  • Step 28 Machining of said roll
  • the roll is preferably treated by a machining step 28 before used in the mill.
  • a machining step 28 for example at the mill an application specific surface treatment of the roll is performed by grinding and other surface treatments to get the desired roughness and the related friction on the surface of the roll.
  • surface treatments of the roll are for example: Laser beam texturing (LBT), Electro beam texturing (EBT) or electro discharge texturing (EDT).
  • the roll is treated by grinding and electro discharge texturing (EDT) surface treatment.
  • EDT electro discharge texturing
  • Figure 15 A-B show microstructure of the surface of a roll comprising a low chromium composition after Electro Discharge Texturing.
  • Figure 15 C-D show microstructure of the surface of the roll according to the invention after Electro Discharge Texturing.
  • Underneath the white layer 300 in figure 15 D there are the re-austenitized layer and a thinner softened zone, since this grade has a high tempering temperature.
  • the eutectic carbides 302 have not been affected by the electric arc energy.
  • these sorts of carbides are not present in the roll described in figure 15 A-B.
  • the roll according to the invention has better properties and performance than a standard grade roll (see figure 15 A-B) due to the presence of the hard eutectic carbides in the white layer.
  • Figure 18 shows a more schematic figure of figure 15D, representing the microstructure of a roll surface according to the invention wherein the newly formed eutectic carbides 302, formed due to the re-melting, are present within the white layer 304. Also previously formed eutectic carbides 300 are shown in figure 18.
  • the roll surface in figure 18 illustrates how the surface looks like after Electro Discharge Texturing according to the invention.
  • the scale 306 represents 5 ⁇ .
  • a roll 1 according to the invention made by the process described above
  • a typical roll according to the invention has a diameter of between 215 and 800 mm or between 250-700mm, total length including the necks is up to 6 meters, wherein the barrel length is between 1-3 meters.
  • the typical weight of the roll is between 400 to 10000kg.
  • the microstructure of a roll according to an embodiment of the invention is characterized in comprising tempered martensite with a retained austenite rate lower than 5% in volume, and wherein the roll comprises an open eutectic carbide network of less than 5 volume % eutectic carbides; and the roll (1) exhibits a hardness between 780 to 840 HV; and internal compressive stresses of between -300 to -500 MPa.
  • the roll according to the invention is intended to be used in a cold strip mill which requires rolls that withstands high pressures.
  • the roll according to the invention is intended to be used in the cold strip mill as a work roll and is suitable in any stand in the rolling process and is suitable in 2H1 to 6Hi mills and may have roughness on the surface from ⁇ .3- ⁇ .5 ⁇ which is required in the finishing stands to a roughness of 1.5-2. 5 ⁇ which is required in the initial stands.
  • the present invention will be understood more readily by reference to the following- examples. However, these examples are intended to illustrate the roll properties of the invention and are not to be construed to limit the scope of the invention.
  • ROLLi according to the invention in table 4 is made using the process according to the invention, using a solidification rate of higher than i5°C/min in the working layer during the solidification interval and also using the induction heating using a frequency of 50-250 HZ and tempering 3 times at 450-530 0 C.
  • ROLL2 according to the invention in table 4 is made using the process according to the invention, using a solidification rate of l8°C/min in the working layer during the
  • Figure 19 shows the microstructure of a roll after tempering and induction hardening, sampled on 4mm depth from the surface of ROLL 2.
  • the microstructure 1034 with the open eutectic network and the eutectic carbides 1032 of the roll is also shown in figure 19.
  • FIG 16 A-D shows detrimental defects 502 on a roll generated during manufacturing of rolls with low chromium content.
  • the detrimental defects 502 are for example porosities and shrinkage.
  • the Mn content for the rolls in table 4 are all within the range 0.4-0.5, Si content for the rolls in table 4 are all within the range 0.2-2,0, Ni is always below 1%.
  • the forged roll according to the invention is suitable to be used for example as a work roll or intermediate roll in cold rolling mills or in for example;
  • the rolls according to the invention exhibit an increased ability to keep their surface texture due to a white layer of the roll and wherein the white layer comprises hard eutectic carbides as M 7 C 3 .
  • the roughness transfer of the roll surface changes during usage of the roll.
  • the rolls according to the invention exhibit an increased ability to keep roughness transfer constant during rolling which is important for the life time of the roll. This is due to the special claimed composition and also due to the production method used when making the rolls.
  • the roll according to the inventions has a strong surface due to that the microstructure of the roll of the invention comprises tempered martensite with a retained austenite rate lower than 5% in volume and carbides as MC and M 2 C finely and homogeneously distributed into the matrix, where M indicates metal and C indicates carbon.
  • This special microstructure increases the possibilities for a schedule-free rolling.
  • Another problem with known rolls is that propagation of cracks inside the rolls is governed by the accumulative stresses, induced by the rolling operation and the field of residual internal stresses of the roll.
  • a roll in service is submitted to a complex set of stresses.
  • the roll according to the invention displays a low level of residual internal stresses and thus a better resistance to spalling and this makes the mill incident rate low.
  • the mechanical strength of the roll of the invention is better compared to a roll with the same alloy composition as the roll of the invention but made using another production method.
  • the mechanical strength of the roll according to the invention is due to the formed open eutectic network in the working layer of the roll. This open eutectic network is formed during the cooling step in the roll-making process. A solidification rate higher than l5°C/min during the cooling step when making the ingot is crucial for the formation of the open network which is present in the rolls according to the invention.
  • the accumulation of various tempering treatments at high temperature after hardening induces an important relaxation of internal stresses of the roll.
  • the internal stresses are minimized by using differential heating of the external layer.
  • the hardness penetration depth of the roll according to the invention can be controlled between 20 and 120 mm on diameter measured from the roll surface and inwards.
  • the internal compressive stresses of the roll of the invention are preferably between -300 to -500 MPa in absolute value or for example lower than -400 MPa.
  • FIG 17A shows a schematic view of an exemplified roll microstructure according to the invention.
  • dendrite arms 210 comprising of eutectic carbides forming the eutectic cell structures 204 by forming an open carbide network.
  • the open eutectic network comprising of dendrite arms 210 forming eutectic cells 204, which can be seen in figure 17A, is formed in the process due to the specific chemical composition according to the invention.
  • the scale 208 represents ⁇ .
  • the microstructure of the roll of the invention comprises an open eutectic network which is only spread over one grain or two grains of the cell structures.
  • figure 17B shows a closed eutectic network wherein the eutectic carbides 200 form a closed eutectic network with clearly separated eutectic cells 212.
  • This type of network is unwanted in the roll according to the invention due to brittleness of the roll if it comprises this type of microstructure.
  • the scale 214 represents ⁇ .

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Heat Treatment Of Articles (AREA)
  • Reduction Rolling/Reduction Stand/Operation Of Reduction Machine (AREA)
  • Heat Treatment Of Steel (AREA)

Abstract

L'invention concerne en général le domaine des rouleaux forgés et la production de rouleaux forgés. Plus particulièrement, la présente invention concerne des rouleaux forgés destinés à être utilisés dans l'industrie du laminage à froid. La présente invention concerne un rouleau forgé destiné à être utilisé dans l'industrie du laminage à froid et un procédé de production d'un tel rouleau. Ledit rouleau forgé comprend une composition d'acier et une microstructure qui comprend : - de la martensite revenue présentant une teneur en austénite retenue inférieure à (<) 5 % par volume; et - un réseau de carbure eutectique ouvert présentant une teneur en carbures eutectiques inférieure à (<) 5 % par volume; le rouleau présentant: -une dureté comprise entre 780 et 840HV; et -une compression interne comprise entre -300 et -500 MPa en valeurs absolues.
PCT/SE2011/050246 2011-03-04 2011-03-04 Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau Ceased WO2012121630A1 (fr)

Priority Applications (5)

Application Number Priority Date Filing Date Title
RU2013142706/02A RU2572269C2 (ru) 2011-03-04 2011-03-04 Кованый валок, соответствующий требованиям производства холоднокатаных изделий и способ получения такого валка
CA2828894A CA2828894C (fr) 2011-03-04 2011-03-04 Rouleau forge satisfaisant les exigences de l'industrie du laminage a froid et procede de production d'un tel rouleau
CN201180000136.7A CN103108975B (zh) 2011-03-04 2011-03-04 满足冷轧工业需求的锻造辊及其生产方法
PCT/SE2011/050246 WO2012121630A1 (fr) 2011-03-04 2011-03-04 Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau
AU2011361937A AU2011361937B2 (en) 2011-03-04 2011-03-04 A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/SE2011/050246 WO2012121630A1 (fr) 2011-03-04 2011-03-04 Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau

Publications (1)

Publication Number Publication Date
WO2012121630A1 true WO2012121630A1 (fr) 2012-09-13

Family

ID=46798429

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/SE2011/050246 Ceased WO2012121630A1 (fr) 2011-03-04 2011-03-04 Rouleau forgé satisfaisant les exigences de l'industrie du laminage à froid et procédé de production d'un tel rouleau

Country Status (5)

Country Link
CN (1) CN103108975B (fr)
AU (1) AU2011361937B2 (fr)
CA (1) CA2828894C (fr)
RU (1) RU2572269C2 (fr)
WO (1) WO2012121630A1 (fr)

Cited By (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN104313477A (zh) * 2014-10-10 2015-01-28 绵阳西诺特矿用设备制造有限公司 一种高耐磨钢材及其应用
WO2016034390A1 (fr) * 2014-09-01 2016-03-10 Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. Corps moulés à haute résistance, absorbant l'énergie mécanique et résistants à la corrosion composés d'alliages de fer et procédé de production desdits corps moulés à haute résistance
CN108350557A (zh) * 2015-10-29 2018-07-31 圣保罗国家技术研究院 铸造工具钢的活塞环及其制造工艺
CN112792304A (zh) * 2020-12-07 2021-05-14 邢台德龙机械轧辊有限公司 大型铬合金带钢支承辊的制备方法
US20220243296A1 (en) * 2021-02-01 2022-08-04 L.E. Jones Company Martensitic Wear Resistant Alloy Strengthened Through Aluminum Nitrides

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106191703A (zh) * 2016-08-16 2016-12-07 安徽瑞泰新材料科技有限公司 一种高铬耐磨钢球及其制备方法
KR102218420B1 (ko) * 2019-07-16 2021-02-19 주식회사 포스코 단조롤 기반 히트 파이프롤 및 그 제조방법
CN111593259B (zh) * 2020-05-20 2021-11-23 樟树市兴隆高新材料有限公司 一种气门钢及其制备方法
CN112410673B (zh) * 2020-11-18 2023-01-31 宝钢轧辊科技有限责任公司 超高强度钢板轧制用高速钢轧辊及其制造方法
CN115074625B (zh) * 2022-06-23 2023-05-09 宝钢轧辊科技有限责任公司 森吉米尔轧机一中间辊及其制造方法

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59179762A (ja) * 1983-03-30 1984-10-12 Daido Steel Co Ltd 冷間ダイス鋼
JPH01208437A (ja) * 1988-02-13 1989-08-22 Kanto Tokushu Seiko Kk 研削性を改善した高クロム型圧延用ロール鋼
JPH06212253A (ja) * 1993-03-30 1994-08-02 Daido Steel Co Ltd 冷間工具鋼の製造方法
EP0869196A2 (fr) * 1997-03-31 1998-10-07 Daido Tokushuko Kabushiki Kaisha Outil coulé et procédé pour sa fabrication

Family Cites Families (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5225007A (en) * 1990-02-28 1993-07-06 Hitachi Metals Ltd. Method for wear-resistant compound roll manufacture
DE4143012C2 (de) * 1991-12-24 1993-11-25 Thyssen Edelstahlwerke Ag Verwendung eines Stahls für Kaltwalzen
GB2367075A (en) * 1999-02-26 2002-03-27 Kanto Special Steel Works Ltd Roll for rolling
CN100404720C (zh) * 2005-03-29 2008-07-23 宝钢集团常州轧辊制造公司 用于制造冷轧工作辊的合金及其制造方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS59179762A (ja) * 1983-03-30 1984-10-12 Daido Steel Co Ltd 冷間ダイス鋼
JPH01208437A (ja) * 1988-02-13 1989-08-22 Kanto Tokushu Seiko Kk 研削性を改善した高クロム型圧延用ロール鋼
JPH06212253A (ja) * 1993-03-30 1994-08-02 Daido Steel Co Ltd 冷間工具鋼の製造方法
EP0869196A2 (fr) * 1997-03-31 1998-10-07 Daido Tokushuko Kabushiki Kaisha Outil coulé et procédé pour sa fabrication

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2016034390A1 (fr) * 2014-09-01 2016-03-10 Leibniz-Institut Für Festkörper- Und Werkstoffforschung Dresden E.V. Corps moulés à haute résistance, absorbant l'énergie mécanique et résistants à la corrosion composés d'alliages de fer et procédé de production desdits corps moulés à haute résistance
CN104313477A (zh) * 2014-10-10 2015-01-28 绵阳西诺特矿用设备制造有限公司 一种高耐磨钢材及其应用
CN108350557A (zh) * 2015-10-29 2018-07-31 圣保罗国家技术研究院 铸造工具钢的活塞环及其制造工艺
CN108350557B (zh) * 2015-10-29 2020-05-12 圣保罗国家技术研究院 铸造工具钢的活塞环及其制造工艺
CN112792304A (zh) * 2020-12-07 2021-05-14 邢台德龙机械轧辊有限公司 大型铬合金带钢支承辊的制备方法
US20220243296A1 (en) * 2021-02-01 2022-08-04 L.E. Jones Company Martensitic Wear Resistant Alloy Strengthened Through Aluminum Nitrides
US11566299B2 (en) * 2021-02-01 2023-01-31 L.E. Jones Company Martensitic wear resistant alloy strengthened through aluminum nitrides
US12018343B2 (en) 2021-02-01 2024-06-25 L.E. Jones Company Martensitic wear resistant alloy strengthened through aluminum nitrides

Also Published As

Publication number Publication date
AU2011361937A1 (en) 2013-10-03
RU2013142706A (ru) 2015-04-10
CA2828894C (fr) 2017-05-09
CA2828894A1 (fr) 2012-09-13
CN103108975A (zh) 2013-05-15
AU2011361937B2 (en) 2015-10-01
RU2572269C2 (ru) 2016-01-10
CN103108975B (zh) 2015-11-25

Similar Documents

Publication Publication Date Title
US8920296B2 (en) Forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll
AU2011361937B2 (en) A forged roll meeting the requirements of the cold rolling industry and a method for production of such a roll
CN103276298B (zh) 高硬高韧冷热兼作模具钢及其生产方法
CN101596553B (zh) 一种应用于高速线材轧机的高速钢辊环及其制造方法
CA3217486A1 (fr) Acier pour arbre d&#39;engrenage cemente a haute temperature et procede de fabrication d&#39;acier
CN100423858C (zh) 焊接钢管用铸造高铬铁或铸造高铬钢轧辊
CN104388821B (zh) TiC粒子增强型复相组织高塑性耐磨钢板及制造方法
WO2016079978A1 (fr) Feuille d&#39;acier épaisse, haute dureté, haute ténacité ayant une excellente uniformité de matière et son procédé de fabrication
EP2495340B1 (fr) Rouleau forgé répondant aux exigences de l&#39;industrie du roulage à froid et procédé de production d&#39;un tel rouleau
CN107073570A (zh) 复合铸造异型轧辊及其制备方法
EP2546374A1 (fr) Acier pour outils d&#39;extrusion
CN102268588A (zh) 钢管减径机或定径机球墨铸铁轧辊及其制备方法
CN112553538A (zh) 一种低硬度20CrMnTi圆钢
JP6114682B2 (ja) 冷間圧延工業の要件を満たす鍛造ロールおよび該ロールの製造方法
CN116623081A (zh) 高碳合金钢及其制备方法和在锯刃工具中的应用
JP2012184471A (ja) 冷間圧延工業の要件を満たす鍛造ロールおよび該ロールの製造方法
KR101305410B1 (ko) 냉간 압연 분야의 필요조건을 충족하는 단조 롤과 그 제조 방법
CN115717212B (zh) 一种齿轴用钢及其制造方法
CN105420629B (zh) 适用于高速线材轧制的高塑性硬质材料辊环及制造方法
CN115287554A (zh) 一种切割工具用高强度合金钢及其热轧卷板的制造方法
Shcherbedinskii Iron: a promising material of the XXI century
CN105177426A (zh) 正火轧制的耐高温容器板及其生产方法
RU2828779C2 (ru) Сталь для высокотемпературного цементированного вала шестерни и способ изготовления такой стали
TWI471420B (zh) 符合冷軋產業規定之鍛造輥及製造此輥之方法
BRPI1101419A2 (pt) um rolo forjado que satisfaz os requerimentos da industria de laminaÇço a frio e um mÉtodo para a produÇço de tal rolo

Legal Events

Date Code Title Description
WWE Wipo information: entry into national phase

Ref document number: 201180000136.7

Country of ref document: CN

121 Ep: the epo has been informed by wipo that ep was designated in this application

Ref document number: 11860604

Country of ref document: EP

Kind code of ref document: A1

ENP Entry into the national phase

Ref document number: 2828894

Country of ref document: CA

NENP Non-entry into the national phase

Ref country code: DE

ENP Entry into the national phase

Ref document number: 2011361937

Country of ref document: AU

Date of ref document: 20110304

Kind code of ref document: A

ENP Entry into the national phase

Ref document number: 2013142706

Country of ref document: RU

Kind code of ref document: A

122 Ep: pct application non-entry in european phase

Ref document number: 11860604

Country of ref document: EP

Kind code of ref document: A1