WO2012053237A1 - Outil de coupe formé de carbure cimenté à base de wc possédant une résistance élevée aux défauts afin de couper un alliage résistant à la chaleur, et outil de coupe formé de carbure cimenté à base de wc dont la surface est revêtue - Google Patents

Outil de coupe formé de carbure cimenté à base de wc possédant une résistance élevée aux défauts afin de couper un alliage résistant à la chaleur, et outil de coupe formé de carbure cimenté à base de wc dont la surface est revêtue Download PDF

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WO2012053237A1
WO2012053237A1 PCT/JP2011/057936 JP2011057936W WO2012053237A1 WO 2012053237 A1 WO2012053237 A1 WO 2012053237A1 JP 2011057936 W JP2011057936 W JP 2011057936W WO 2012053237 A1 WO2012053237 A1 WO 2012053237A1
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cemented carbide
based cemented
cutting tool
particles
content
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PCT/JP2011/057936
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English (en)
Japanese (ja)
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亮介 山口
田代　安彦
正典 齋藤
岡田　一樹
和裕 秋山
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三菱マテリアル株式会社
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    • 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
    • B22F2999/00—Aspects linked to processes or compositions used in powder metallurgy
    • 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
    • B22F7/06—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 workpieces or articles from parts, e.g. to form tipped tools

Definitions

  • the present invention relates to a cutting tool made of a WC-based cemented carbide (hereinafter referred to as a WC-based cemented carbide tool) that exhibits excellent fracture resistance over long-term use in cutting of heat-resistant alloys such as Ni-based alloys and Co-based alloys. And a surface-coated WC-based cemented carbide cutting tool (hereinafter referred to as a coated WC-based cemented carbide tool).
  • a WC-based cemented carbide tool a surface-coated WC-based cemented carbide cutting tool
  • a cutting tool having excellent wear resistance for example, a WC-based cemented carbide containing Co as a binder phase forming component and the remainder consisting of WC and unavoidable impurities, or VC, Cr3C2, TiC
  • a WC-based cemented carbide tool made of a WC-based cemented carbide containing at least one selected from TaC and NbC is known.
  • Re is further added as an alloy component.
  • WC-based carbide tools have also been developed.
  • a WC-based cemented carbide tool (referred to as a conventional cemented carbide tool 1) is manufactured.
  • the conventional cemented carbide tool 1 as shown in FIG. 2, the entire interior of the WC particles constituting the hard phase is covered. It is known that about 0.1 to 3 wt% of Re is dissolved in a substantially uniform manner, and by providing such a structure, excellent toughness is exhibited.
  • Patent Document 2 discloses that a WC-based cemented carbide tool is produced by solid-phase sintering a WC-based cemented carbide containing 25 wt% or more of Re in the binder phase. As shown in FIG. 3, it is known that a base carbide tool (conventional carbide tool 2) is improved in high-temperature hardness because a high melting point Re component exists in the binder phase.
  • the present inventors from the above viewpoint, exhibit excellent fracture resistance and heat plastic deformation even when used for cutting heat-resistant alloys such as Ni-base alloys and Co-base alloys, As a result of earnest research on a WC-based carbide tool that exhibits excellent cutting performance over a long period of use, the following knowledge was obtained.
  • a sintered body made of a WC-based cemented carbide is manufactured by using VC powder, Cr3C2 powder, TiC powder, TaC powder, and NbC powder as needed together with WC powder and Co powder having a specific average particle diameter.
  • the raw material powders blended in proportions are mixed and molded in a wet ball mill, and then the green compact is manufactured by sintering at a predetermined temperature for a predetermined time.
  • the present inventors for example, in addition to Co powder as a binder phase forming component, have a predetermined average particle size and a predetermined content ratio.
  • a raw material powder is prepared by further adding and mixing Re powder, and this is liquid-phase sintered at a temperature within a range of 1380 to 1500 ° C. Further, hot isostatic pressure in a predetermined pressurized atmosphere Re-enriched regions are formed in the vicinity of the interface in the WC grains constituting the hard phase by press (HIP) molding and then cooling, for example, to at least 900 ° C. at a rate of 10 ° C./min or more.
  • HIP press
  • the Re-enriched region contains Re having an average Re content of 0.2 to 7% by mass from the interface of the WC particles to a depth region of 1 to 10% of the particle diameter of the WC particles.
  • the average Re content is less than 0.2% by mass.
  • a WC-based cemented carbide tool made of a WC-based cemented carbide having a sintered structure containing the WC particles in which the Re-enriched region is formed in the vicinity of the interface in the WC grain (hereinafter referred to as the present invention
  • cutting of heat-resistant alloys such as Ni-base alloys and Co-base alloys with high heat generation suppresses overheating of the cutting edge and provides excellent fracture resistance. It has been found that it exhibits heat-resistant plastic deformation and, as a result, exhibits excellent cutting performance over a long period of use without occurrence of chipping, uneven wear, and the like.
  • This invention has been made based on the above findings, “(1) Made of WC-based cemented carbide containing Co as a binder phase component, Re as an additive component, and WC-based cemented carbide consisting of WC as a hard-phase component and unavoidable impurities as a tool base.
  • the content of Co as a binder phase component is 4 to 12% by mass
  • Re is dissolved in the binder phase
  • the Re content in the binder phase is 3 to 20% by mass.
  • a WC-based cemented carbide cutting tool comprising WC particles in which a Re-enriched region is formed in the vicinity of an interface in a WC grain constituting a hard phase.
  • the total of WC particles containing Re as a whole is included in 90% by number or more of all WC particles in the WC-base cemented carbide cutting tool base, as described in (3) above WC-based cemented carbide cutting tool.
  • the Re-enriched region is formed from the interface of the WC particles to a depth region of 1 to 10% of the particle diameter of the WC particles, and the average Re content in the depth region is 0.
  • the WC according to any one of (1) to (4) above, wherein the average Re content is less than 0.2% by mass on the inner side of the WC particles.
  • the WC-based cemented carbide cutting tool base further contains a total of 0.1 to 2% by mass of one or more selected from VC, Cr3C2, TiC, TaC, and NbC.
  • the WC-based carbide tool of the present invention will be described in detail below.
  • the WC-based cemented carbide tool of the present invention includes, for example, Re powder in addition to WC powder and Co powder, and further, VC powder, Cr3C2 powder, TiC powder, TaC powder, and NbC powder as required. After mixing the raw material powder blended so as to be in a wet ball mill and press-molding it into a predetermined shape, this compacted body is subjected to a predetermined temperature within a range of 1380 to 1500 ° C. in a vacuum of 1 to 15 Pa.
  • 3 to 20% by mass of Re is solid-solved in the binder phase, and the particle size of the WC particles is reduced from the interface of the WC particles.
  • WC particles in which an enriched region of Re having an average Re content of 0.2 to 7% by mass is formed over a depth region of 1 to 10%, and inside the Re enriched region That is, the average Re content is less than 0.2% by mass on the inner side of the WC particles.
  • Re is mainly present in the vicinity of the WC particle interface, the thermal conductivity of the WC particles is not greatly reduced. Since Re is solid-solved in the inside, the high-temperature hardness of the binder phase is improved, and the Re-enriched region formed in the vicinity of the interface in the WC grain improves the adhesion strength between the WC particle and the binder phase. Enhanced.
  • the Co component constituting the binder phase in the WC-based cemented carbide tool of the present invention is less than 4% by mass, the WC-based cemented carbide will not be sufficiently densified, while the binder phase content is 12%. If the mass% is exceeded, the hardness of the WC-based cemented carbide decreases, and the wear resistance tends to decrease in the cutting of heat-resistant alloys such as Ni-based alloys and Co-based alloys.
  • the binder phase content in the cemented carbide sintered body was determined to be 4 to 12% by mass.
  • the Re powder blended together with the WC powder and the Co powder is mostly dissolved (3 to 20% by mass) in Co constituting the binder phase, and a part thereof is contained in the vicinity of the interface in the WC grain.
  • the Re content (Re / (Co + Re)) which forms a Re-enriched region, is less than 3% by mass, the effect of improving the adhesion between the WC grains and the binder phase and the hardness of the binder phase
  • the Re content (Re / (Co + Re)) dissolved in Co exceeds 20% by mass, the toughness of the binder phase is remarkably reduced, and the fracture toughness value is lowered. Since chipping is likely to occur during cutting of the alloy, the Re content (Re / (Co + Re)) that is dissolved in Co is determined to be 3 to 20% by mass.
  • a Re-enriched region is formed in the vicinity of the interface in the WC grain, and the Re-enriched area is formed over a depth region of 1 to 10% of the grain size of the WC particle, and
  • the average Re content (Re / (W + Re)) in the depth region is 0.2 to 7% by mass, but the Re content in the depth region of 1 to 10% of the particle size of the WC particles is 0.1%. If it is less than 2% by mass, the effect of improving the adhesion between the WC grains and the binder phase cannot be obtained.
  • the average Re content (Re / (W + Re)) in the Re-enriched region that is, the depth region of 1 to 10% of the WC particle diameter. ) was determined to be 0.2 to 7% by mass.
  • the depth region of 1 to 10% of the particle diameter of the WC particle is defined by another expression, the WC observed with a scanning electron microscope (SEM) equipped with a backscattering electron diffractometer (EBSD).
  • SEM scanning electron microscope
  • EBSD backscattering electron diffractometer
  • the WC grains and the binder phase are included even if the WC grains containing Re are contained in the entire WC grains.
  • the content exceeds 30% by number of all the WC particles, the thermal conductivity is remarkably lowered, so that the cutting edge is likely to be overheated. Since it tends to occur, the content of WC particles containing Re in the entire WC grain is determined to be 30% by number or less of all WC grains.
  • the total content of the WC particles in which the Re-enriched region is formed in the vicinity of the interface in the WC particles and the WC particles in which the Re is contained in the entire WC particles is less than 90% of all the WC particles. Then, since the effect of improving the adhesion between the WC grains and the binder phase cannot be obtained, the WC grains in which a Re-enriched region is formed in the vicinity of the interface in the WC grains and the WC grains containing Re in the entire WC grains. The total content of was determined to be 90% by number or more of all WC particles.
  • the WC-based carbide tool of the present invention can contain one or more components selected from VC, Cr3C2, TiC, TaC, and NbC. Any one or two or more components selected from VC, Cr3C2, TiC, TaC, and NbC have the effect of suppressing grain growth of WC during sintering, but the total content is 0. If it is less than 1% by mass, the effect of inhibiting grain growth is small. On the other hand, if it exceeds 2% by mass, a composite carbide phase precipitates and the hardness tends to decrease. Therefore, VC, Cr3C2, TiC, TaC, NbC The content of one or more components selected from among them was determined to be 0.1 to 2% by mass in total.
  • the WC-based cemented carbide tool of the present invention can be used as a cutting tool as it is, but by further forming a hard coating layer on the surface thereof, further improving the fracture resistance and the heat plastic deformation resistance.
  • the tool life can be further extended.
  • the hard coating layer is, for example, “at least one element selected from the group consisting of IVa group element, Va group element, VIa group element, Al, B and Si of the periodic table, carbon, nitrogen And a compound containing at least one element selected from the group consisting of oxygen, and more specifically, for example, Ti carbide, nitride, carbonitride, Ti and Al composite nitride, It consists of one kind of single layer or two or more kinds of multilayers selected from a composite nitride of Al and Cr, a composite nitride of Ti and Si, and a composite nitride of Ti, Al and Si.
  • the WC-based cemented carbide tool and the surface-coated WC-based cemented carbide tool according to the present invention include a WC-based cemented carbide alloy constituting the WC-based cemented carbide in which the Re is dissolved and the high-temperature hardness is increased.
  • a WC-based cemented carbide alloy constituting the WC-based cemented carbide in which the Re is dissolved and the high-temperature hardness is increased.
  • the schematic diagram of the sintered compact structure in this invention WC group carbide tool is shown.
  • the schematic diagram of the sintered compact structure in the conventional WC base carbide tool (conventional carbide tool 1) is shown.
  • the schematic diagram of the sintered compact structure in another conventional WC group carbide tool (conventional carbide tool 2) is shown.
  • Co powders, Re powders, VC powders, Cr3C2 powders, TiC powders, TaC powders, NbC powders, and WC powders, all having an average particle diameter of 0.5 to 5 ⁇ m, are prepared as raw material powders.
  • B These green compacts are held at a sintering temperature shown in Table 2 for 1 hour in a vacuum of 1.3 Pa, and then Ar gas is introduced into the furnace to form a 6 MPa pressurized atmosphere.
  • the obtained round bar sintered body having a predetermined diameter is processed so as to have a predetermined size, and processed so as to have the cutting edge portion dimensions shown in Table 3, and is a table composed of a 6-blade square end mill.
  • Cutting tools 1 to 10 made of the WC-based cemented carbide of the present invention (referred to as the present cemented carbide tool) 1 to 10 shown in FIG.
  • a hard coating layer having the composition and average film thickness as shown in Table 4 is vapor-deposited on the surface of the tool base using an arc ion plating apparatus.
  • a cutting tool made of the surface-coated WC-based cemented carbide of the present invention was produced.
  • the raw material powder is blended so as to have the blending composition shown in Table 1, and the cutting edge dimensions shown in Table 3 are obtained by the same process as the cemented carbide tools 1 to 10 of the present invention.
  • Processing was carried out to produce comparative example WC-based cemented carbide cutting tools (referred to as comparative example cemented carbide tools) 11 to 20 shown in Table 5 consisting of a 6-blade square end mill.
  • a hard coating layer having a composition and an average film thickness as shown in Table 4 is vapor-deposited on the tool base surface using an arc ion plating apparatus.
  • a comparative example surface-coated WC-based cemented carbide cutting tool was produced.
  • the above-mentioned carbide tools 1 to 10 of the present invention and comparative carbide tools 12, 14, 17, and 20 were obtained by observing with a scanning electron microscope (SEM) equipped with a backscattering electron diffractometer (EBSD).
  • SEM scanning electron microscope
  • EBSD backscattering electron diffractometer
  • the area of the WC grain was measured by image analysis of the crystal orientation mapping image of the WC grain, and the diameter when the WC was approximated to a circle having the same area was calculated.
  • TEM transmission electron microscope
  • EDS energy dispersive X-ray analyzer
  • the Re content of the phase, the average Re content in the WC grains, and the thickness ratio (%) of the Re-enriched area (area where the Re content is 0.2 to 7% by mass) in the WC grain size It was measured.
  • Table 6 shows the average value of the measurement results of 50 WC particles, the number of WC particles in which a Re-enriched region is formed in a depth region of 1 to 10% of the WC particle size, and Re in the entire WC particle.
  • the number of WC particles contained and the average value of the Re content in the Re-enriched region are shown.
  • the content of WC particles containing Re in the entire WC grain is 30% by number or less, and in a depth region of 1 to 10% of the WC grain size.
  • the WC particles in which the Re-enriched regions are formed and the WC particles in which Re is contained in the entire WC grains are contained in a total of 90% by number or more.
  • the average Re content in the enriched regions is 0.2 to It was within the range of 7% by mass.
  • FIG. 1 the schematic diagram of the sintered compact structure
  • the comparative cemented carbide tools 12 and 20 had a large amount of Re powder, so that the Re enriched region was formed.
  • the average Re content in the enriched region is the amount specified in the present invention.
  • the number of WC particles containing Re in the entire WC grains exceeded the amount specified in the present invention.
  • the Re enriched region was formed, but the number of WC particles in which the enriched region was formed and the Re in the entire WC grain.
  • the total number of WC particles contained was below the amount specified in the present invention, and the average Re content in the enriched region was below the amount specified in the present invention.
  • a square material of a Ni-base alloy heat-resistant alloy (Cr: 18.5%, Mo: 3.0%, Al: 0.5%, Nb + Ta: 5.1%, balance: Ni and inevitable impurities) is used as a work material.
  • a cutting test was performed under the various conditions shown in Fig. 3, and the cutting length until the flank wear width at the tip of the outer peripheral blade reached the value of the standard for use was measured. Moreover, this was observed about the abrasion condition of the cutting edge after a cutting test. The measurement results and observation results are shown in Table 5.
  • the binder phase of the WC-based cemented carbide sintered body contains 3 to 20% by mass of solid solution Re and is hard.
  • the average Re content in the Re-enriched region is 0.2 to 7% by mass, and the high temperature hardness is improved without causing a decrease in thermal conductivity, and the adhesion between the binder phase and the hard phase is improved.
  • Co powders, Re powders, VC powders, Cr3C2 powders, TiC powders, TaC powders, NbC powders, and WC powders, all having an average particle diameter of 0.5 to 5 ⁇ m, are prepared as raw material powders.
  • the powder was blended into the blending composition shown in Table 7, added with wax, wet mixed with a ball mill for 72 hours, dried under reduced pressure, and then pressed into a predetermined shape at a pressure of 100 MPa,
  • B These green compacts are held at a sintering temperature shown in Table 8 in a vacuum of 1.3 Pa for 1 hour, and then Ar gas is introduced into the furnace to form a pressurized atmosphere of 6 MPa. For 1 hour, and then cooled to 900 ° C.
  • the raw material powder was blended so as to have the blending composition shown in Table 7, and in the same manner as the cemented carbide tools 21 to 28 of the present invention, the comparative cemented carbide tool 31 having the insert shape of APMT1604PDER. ⁇ 38 were produced.
  • a hard coating layer having the composition and average film thickness as shown in Table 4 is vapor-deposited on the tool base surface using an arc ion plating apparatus. As a result, a comparative example surface-coated WC-based cemented carbide cutting tool was produced.
  • each of the cemented carbide tools 21 to 28 of the present invention a total of 90% by number or more of WC particles in which an enriched region of Re is formed in the vicinity of the interface in the WC grains and WC particles containing Re in the entire WC grains.
  • the average Re content in the Re-enriched region was in the range of 0.2 to 7% by mass.
  • each of the comparative carbides 33, 34, and 37 has the number of WC particles in which the Re-enriched region is formed in the vicinity of the interface in the WC grain, and the average Re content in the Re-enriched region. All were outside the range of the amount specified in the present invention.
  • each of the cemented carbide tools 21 to 28 of the present invention and the comparative example cemented carbide tools 31 to 38 were fixed with screws to a cutter made of an alloy steel having a diameter of 32 mm, and a cutting test was performed under the following conditions.
  • Work Material Ni-base alloy heat-resistant alloy (Cr: 18.5%, Mo: 3.0%, Al: 0.5%, Nb + Ta: 5.1%, balance: Ni and inevitable impurities),
  • Cutting speed 40 m / min
  • Radial depth of cut 1.0 mm
  • Feeding 0.15mm / tooth
  • Table 9 shows the measurement results and the observation results.
  • the binder phase of the WC-based cemented carbide sintered body contains 3 to 20% by mass of solid solution Re and is hard.
  • the average Re content in the Re-enriched region is 0.2 to 7% by mass, and the high temperature hardness is improved without causing a decrease in thermal conductivity, and the adhesion between the binder phase and the hard phase is improved.
  • the comparative carbide tools 31 to 38 have cutting edges when used for cutting heat-resistant alloys such as Ni-base alloys and Co-base alloys whose cutting edges are locally exposed to high temperatures. It is clear that the defect of the part occurs and the service life is reached in a relatively short time.
  • the WC-based cemented carbide cutting tool and the surface-coated WC-based cemented carbide cutting tool according to the present invention are not only used for cutting heat-resistant alloys such as Ni-based alloys and Co-based alloys, but also for various steels and cast irons.
  • the present invention can be applied to cutting under the above conditions, and exhibits excellent cutting performance over a long period of use, and is suitable for labor saving and energy saving of cutting work and further cost reduction.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
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Abstract

La présente invention concerne un outil de coupe possédant une résistance élevée aux défauts au cours d'une longue période d'utilisation dans le cadre d'un procédé de coupe et de laminage d'un alliage résistant à la chaleur, tel un alliage à base de Ni ou de Co. L'invention porte donc sur un outil de coupe formé de carbure cimenté à base de WC dans lequel la teneur du composant Co en phase de liaison est comprise entre 4 et 12 % en masse et la teneur en Re en phase de liaison est comprise entre 3 et 20 % en masse. La surface enrichie en Re est formée à proximité de la surface interne d'un grain de WC en phase dure, à partir de la surface du grain de WC sur toute une zone présentant une profondeur comprise entre 1 % et 10 % du diamètre du grain de WC. La teneur moyenne en Re dans ladite zone est comprise entre 0,2 et 7 % en masse et, au besoin, les composants de carbure cimenté, tels que VC, Cr3c2, TiC, TaC et Nbc, peuvent être inclus ou un revêtement dur peut être formé sur la surface de l'outil de coupe par dépôt de vapeur.
PCT/JP2011/057936 2010-10-19 2011-03-30 Outil de coupe formé de carbure cimenté à base de wc possédant une résistance élevée aux défauts afin de couper un alliage résistant à la chaleur, et outil de coupe formé de carbure cimenté à base de wc dont la surface est revêtue WO2012053237A1 (fr)

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Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11502260A (ja) * 1995-03-03 1999-02-23 ケンナメタル インコーポレイテッド 耐蝕性サーメット摩耗部品
JP2004263251A (ja) * 2003-03-03 2004-09-24 Tungaloy Corp ７ａ族元素含有超硬合金

Family Cites Families (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US11005A (en) * 1854-06-06 Berth-knee former

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH11502260A (ja) * 1995-03-03 1999-02-23 ケンナメタル インコーポレイテッド 耐蝕性サーメット摩耗部品
JP2004263251A (ja) * 2003-03-03 2004-09-24 Tungaloy Corp ７ａ族元素含有超硬合金

Cited By (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
RU2521747C1 (ru) * 2012-12-12 2014-07-10 Анатолий Матвеевич Адаскин Твердый сплав на основе карбида вольфрама для обработки резанием труднообрабатываемых материалов
CN103741001A (zh) * 2014-01-16 2014-04-23 河源普益硬质合金厂有限公司 高硬度高强度py30t硬质合金及其合金制品的制备方法
CN107287472A (zh) * 2016-04-13 2017-10-24 沈阳拓普新材料有限公司 钴基含铌含铜粉末冶金法化纤切断刀的制造
CN107955898A (zh) * 2016-10-14 2018-04-24 刘立凡 硬质合金材料及其制造方法
CN106756394A (zh) * 2017-01-09 2017-05-31 株洲精特硬质合金有限公司 超耐磨高硬度硬质合金钻具材料及其制备方法
CN111378857A (zh) * 2018-12-28 2020-07-07 自贡硬质合金有限责任公司 一种高性能超细晶硬质合金制备方法
CN114959400A (zh) * 2022-04-21 2022-08-30 广东翔鹭钨业股份有限公司 高韧性、高硬度的WC-Co硬质合金及其制备方法
CN115305400A (zh) * 2022-08-16 2022-11-08 江西理工大学 一种稀土添加的WC-Co-Al硬质合金及其制备方法

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