[go: up one dir, main page]

WO2022208766A1 - Alliage extra-dur et moule - Google Patents

Alliage extra-dur et moule Download PDF

Info

Publication number
WO2022208766A1
WO2022208766A1 PCT/JP2021/013918 JP2021013918W WO2022208766A1 WO 2022208766 A1 WO2022208766 A1 WO 2022208766A1 JP 2021013918 W JP2021013918 W JP 2021013918W WO 2022208766 A1 WO2022208766 A1 WO 2022208766A1
Authority
WO
WIPO (PCT)
Prior art keywords
particles
cemented carbide
binder phase
less
area
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/JP2021/013918
Other languages
English (en)
Japanese (ja)
Inventor
翔太 青柳
勉 小椋
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.)
Fuji Die Co Ltd
Original Assignee
Fuji Die Co Ltd
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 Fuji Die Co Ltd filed Critical Fuji Die Co Ltd
Priority to JP2021518023A priority Critical patent/JP6900099B1/ja
Priority to PCT/JP2021/013918 priority patent/WO2022208766A1/fr
Publication of WO2022208766A1 publication Critical patent/WO2022208766A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

Links

Images

Classifications

    • 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

Definitions

  • the present invention relates to a cemented carbide and a mold using it.
  • Cemented carbide is often used for the molds used in the processing of metal work materials, especially in the manufacturing and processing of motor cores and lead frames, when wear resistance is emphasized.
  • a mold material not only abrasion resistance but also transverse rupture strength and impact resistance are required to improve chipping resistance.
  • the toughness there is a means of coarsening the WC in addition to increasing the binder phase.
  • coarsening the WC increases the average thickness of the binder phase, which is a metal component, and promotes adhesion to the workpiece. This causes adhesive wear and an increase in machining load.
  • As a countermeasure against this adhesion there is a method of forming a hard film having excellent adhesion resistance to metal components.
  • coating treatment is required each time, which makes it uneconomical.
  • the average grain size of WC is 1.0 to 1.5 ⁇ m, the amount of binder phase is 12 to 15% by mass, and the Vickers hardness is about 1300 to 1450 HV.
  • uncoated cemented carbide is predominantly used, problems of chipping and adhesive wear remain.
  • the demand for improving the performance of motor cores has become conspicuous, and there is a demand for thinner and harder materials to be processed.
  • the fine-grained WC cemented carbide as described above does not have sufficient toughness of the material itself.
  • Patent Document 1 discloses that the average grain size of WC grains of cemented carbide is 2.5 to 4.5 ⁇ m, and the content of WC fine grains having a grain size of less than 1.0 ⁇ m is 5% or less of the total tungsten carbide. Therefore, it is disclosed that it is excellent in impact resistance and abrasion resistance. However, since the content of WC fine particles is as small as 5% or less, it is considered that wear and chipping due to adhesion will become a problem when the work material is metal.
  • Patent document 2 describes a technique for punching a high-silicon steel sheet that tends to cause adhesion by applying a hard film such as TiC or TiCN, which has excellent adhesion resistance to metals, to a cemented carbide with an average WC particle diameter of 3.9 ⁇ m. It also discloses that adhesion is suppressed and chipping is reduced during processing. However, when the wear progresses due to use, the cost is increased because the hard film must be reworked by grinding.
  • a hard film such as TiC or TiCN, which has excellent adhesion resistance to metals
  • the area ratio of roughly polygonal coarse WC particles with a major axis of 2 ⁇ m or more is 5 to 30% of the total tungsten carbide
  • the area ratio of WC fine particles with a major axis of 0.5 ⁇ m or less is 5% to 30% of the total tungsten carbide.
  • Patent Document 4 discloses a WC-Cr-Co-Ni cemented carbide in which WC consists of a fine particle group with a particle size of less than 2 ⁇ m and a coarse particle group with a particle size of 2 ⁇ m or more, and the amount of WC in the coarse particle group with respect to the total amount of WC is the area It discloses a cemented carbide with a proportion of 5-20%. However, chipping is likely to occur because the ratio of WC coarse particles to the total amount of WC is small.
  • an object of the present invention is to provide a cemented carbide having excellent wear resistance and toughness, good chipping resistance, and excellent adhesion resistance.
  • Another object of the present invention is to provide a mold made of such cemented carbide.
  • the present inventors have found that by finely controlling the ratio of WC fine particles and WC coarse particles and the amount of the binder phase, the thick part of the binder phase that causes adhesion to the work material can be reduced. It is possible to obtain a cemented carbide that can be suppressed, has excellent wear resistance and fracture toughness, has good chipping resistance, has excellent adhesion resistance, and is suitable for molds. I thought of it.
  • the most important point of the present invention is that the adhesion to the work material is suppressed by controlling the thick part of the binder phase, not the average thickness of the binder phase of the cemented carbide.
  • cemented carbide adhesion has been discussed in terms of the average thickness of the binder phase.
  • the WC grains are made coarser and the amount of the binder phase is increased. It will be.
  • the present inventors have noted that particularly thick portions of the binder phase tend to adhere to the workpiece.
  • the cemented carbide according to one embodiment of the present invention includes a hard phase containing WC as a main component and a binder phase containing Co as a main component, and the hard phase has a grain size of 1.6 ⁇ m or more and less than 6.0 ⁇ m. and WC fine particles having a particle size of less than 1.6 ⁇ m, the area ratio of the WC coarse particles to the entire WC is 20 to 35 area %, and the area ratio of the WC fine particles is 65 to 80 area % of the entire WC, the content X of the binder phase is 10 to 15 mass % of the entire cemented carbide, and the average grain size of the WC coarse particles is 2 ⁇ m or more and less than 4 ⁇ m. is included in the range, and the average particle size Y of the WC fine particles is expressed by the following formula (1) -0.065X + 1.20 ⁇ Y ⁇ -0.065X +1.70 (1) is characterized by satisfying
  • the area ratio of WC giant particles with a particle size of 6.0 ⁇ m or more is preferably less than 5 area % of the entire WC.
  • the average particle diameter Y of the WC fine particles is expressed by the following formula (2) -0.065X + 1.34 ⁇ Y ⁇ -0.065X + 1.58 (2) is preferably satisfied.
  • the number of particles with a diameter of 2.5 ⁇ m or more is 700/mm 2 or less, and the number of particles with a diameter of 4 ⁇ m or more is 20/mm 2 or less. characterized by being
  • the number of particles constituting the binder phase is preferably 350 particles/mm 2 or less with a diameter of 2.5 ⁇ m or more, and 10 particles/mm 2 or less with a diameter of 4 ⁇ m or more.
  • a mold according to another embodiment of the present invention is characterized by being made of the above cemented carbide.
  • the present invention by finely controlling the average particle size and ratio of the WC fine particles and WC coarse particles and the amount of the binder phase, thick portions of the binder phase that cause adhesion to the workpiece can be suppressed. It is possible to obtain a cemented carbide having excellent wear resistance and fracture toughness, good chipping resistance, and excellent adhesion resistance.
  • the cemented carbide of the present invention is particularly suitable for use in molds.
  • FIG. 4 is a diagram showing the relationship between the amount of binder phase added and the average particle size of WC fine particles.
  • 10 is a SEM photograph showing a polished cross section of the cemented carbide of Example 8.
  • FIG. 10 is a SEM photograph showing a polished cross section of the cemented carbide of Comparative Example 9.
  • FIG. 10 is a SEM photograph showing a polished cross section of the cemented carbide of Comparative Example 9.
  • the cemented carbide of the present invention is a cemented carbide containing a hard phase mainly composed of WC and a binder phase mainly composed of Co, wherein the hard phase is coarse WC particles having a particle size of 1.6 ⁇ m or more and less than 6.0 ⁇ m. and WC fine particles with a particle size of less than 1.6 ⁇ m, the area ratio of the WC coarse particles is 20 to 35 area% of the total WC, and the area ratio of the WC fine particles to the entire WC is 65 to 35%.
  • the content X of the binder phase is 10 to 15% by mass of the entire cemented carbide
  • the average particle size of the WC coarse particles is in the range of 2 ⁇ m or more and less than 4 ⁇ m
  • the average particle size of the WC fine particles is Y is the following formula (1) -0.065X + 1.20 ⁇ Y ⁇ -0.065X + 1.70 (1) is characterized by satisfying
  • the grain size of WC coarse particles is within the range of 1.6 ⁇ m or more and less than 6.0 ⁇ m.
  • the grain size of the WC grains is the diameter of the hard phase in any cross section of the cemented carbide when converted to a circle with the same area. If WC giant particles with a particle size of 6.0 ⁇ m or more are included, the transverse rupture strength is lowered and the thick portion of the binder phase is increased, which is not desirable.
  • the WC macroparticles are preferably less than 5 area %, more preferably 2 area % or less, even more preferably 1 area % or less, relative to the total WC.
  • the grain size of the WC coarse particles is preferably in the range of 1.6 ⁇ m or more and less than 4.5 ⁇ m.
  • the average particle size of WC coarse particles is in the range of 2 ⁇ m or more and less than 4 ⁇ m.
  • the average grain size of WC grains is obtained by dividing the sum of the areas of all WC coarse grains in an arbitrary cross section of the cemented carbide by the number of WC coarse grains. Calculated by converting to the diameter of a circle. If the average grain size of the WC coarse grains is less than 2 ⁇ m, sufficient toughness cannot be obtained and the chipping resistance is lowered. On the other hand, when the average grain size of the WC coarse particles is 4 ⁇ m or more, the transverse rupture strength is lowered and the number of thick portions of the binder phase is increased.
  • the area ratio of WC coarse particles is 20 to 35 area% of the entire WC. If the area ratio of WC coarse particles is less than 20 area %, the effect of improving fracture toughness cannot be sufficiently obtained. On the other hand, if the area ratio of WC coarse particles exceeds 35 area %, the transverse rupture strength becomes too low and the number of thick portions of the binder phase increases.
  • the particle size of WC fine particles is within the range of less than 1.6 ⁇ m.
  • the content X of the binder phase is 10-15% by mass of the entire cemented carbide.
  • the binder phase content X means the total sum of the components added as binder phase components in the binder phase. exclude. If the content X of the binder phase is less than 10% by mass, the hardness of the cemented carbide becomes too high and the toughness decreases. Moreover, when the content X of the binder phase exceeds 15% by mass, the number of thick portions of the binder phase increases.
  • the average particle diameter Y of WC fine particles is expressed by the following formula (1) -0.065X +1.20 ⁇ Y ⁇ -0.065X + 1.70 (1) meet.
  • the lower limit of the average particle size Y of the WC fine particles is preferably -0.065X + 1.34, and the upper limit of the average particle size Y of the WC fine particles is preferably -0.065X + 1.58.
  • the average particle diameter Y of WC fine particles is expressed by the following formula (2) -0.065X + 1.34 ⁇ Y ⁇ -0.065X + 1.58 (2) is preferably satisfied.
  • the area ratio occupied by WC fine particles is 65 to 80% of the total WC. If the area ratio of the WC fine particles is less than 65 area %, the transverse rupture strength becomes too low and the number of thick portions of the binder phase increases. Further, if the area ratio of the WC fine particles exceeds 80 area %, the effect of improving fracture toughness cannot be sufficiently obtained.
  • the thickness of the binder phase the higher the intrinsic strength of the cemented carbide, but if the thickness of the binder phase is too thin, the fracture toughness will decrease, making it more sensitive to defects and lowering the strength.
  • the thickness of the binder phase is small, the fatigue strength of the binder phase due to repeated stress is less likely to occur and the fatigue strength is high.
  • the thickness of the binder phase is large, the toughness is increased, but the material is easily deformed and the fatigue strength tends to decrease. Taking these into consideration, the grain size of the WC fine grains is made finer than before, and the average grain size and area ratio are finely controlled to obtain the optimum alloy for applications where repeated stress is applied.
  • the number of particles with a diameter of 2.5 ⁇ m or more is 700/mm 2 or less, and the number of particles with a diameter of 4 ⁇ m or more is 20/mm 2 or less. is preferred. If the binder phase exceeds 700 particles/ mm2 with a diameter of 2.5 ⁇ m or more or 20 particles/ mm2 with a diameter of 4 ⁇ m or more, adhesion to the work material becomes significant, causing adhesive wear and an increase in load during processing. induced chipping increases. It is preferable that the number of particles with a diameter of 2.5 ⁇ m or more is 350/mm 2 or less, and the number of particles with a diameter of 4 ⁇ m or more is 10/mm 2 or less.
  • the Cr powder may be added directly to the raw material powder of the cemented carbide, but it may also be added as Cr 3 C 2 powder. can be In either case, most of Cr dissolves in Co, and the remainder remains as a solid solution with other carbides.
  • VC may be further added in an amount of 5% by mass or less relative to the total amount of the binder phase.
  • WC phase which is the main component of the hard phase
  • Cr CrC, (W, Ti)C, (W, Cr, Ti)C, (W, Ti)CN, (W, Ti, Nb)C and the like.
  • the binder phase may contain 30% by mass of Ni in addition to Co, which is the main component, and if it is 20% by mass, the advantages can be brought out without further degrading the properties.
  • it may contain components such as Fe, Al, and Cu that can be used as a binder phase. These components correspond to the components added as the binder phase components described above.
  • the metal elements forming the hard phase are dissolved in the binder phase of the cemented carbide.
  • the Vickers hardness of the cemented carbide is preferably 1300 to 1450 HV. If the Vickers hardness is less than 1300 HV, the hardness is insufficient, and if the Vickers hardness is more than 1450 HV, chipping tends to occur. More preferably, the cemented carbide has a Vickers hardness of 1300-1400 HV.
  • the cemented carbide has a transverse rupture strength of 3200 MPa or more.
  • Transverse rupture strength is determined by a three-point bending test based on JIS R 1601. If the transverse rupture strength is less than 3200 MPa, breakage and chipping are likely to occur. More preferably, the cemented carbide has a transverse rupture strength of 3500 MPa or more.
  • the fracture toughness value K IC which indicates the toughness of the cemented carbide, is preferably 20 MPa ⁇ m 1/2 or more.
  • the fracture toughness value K IC is calculated based on JIS R 1607 from the crack length generated at the Vickers indentation corner. When the fracture toughness value K IC is less than 20 MPa ⁇ m 1/2 , chipping tends to occur.
  • cemented carbide manufacturing method An example of the cemented carbide manufacturing method is described below. After wet-mixing the raw material powders in a ball mill or the like, the mixture is dried to prepare a molding powder that will be a raw material for a cemented carbide.
  • a molding powder that will be a raw material for a cemented carbide.
  • the binder phase component powder fine particle powder having an average particle size of less than 1 ⁇ m may be used, or oxide powder may be used.
  • the molding powder is molded by methods such as mold molding and cold isostatic pressing (CIP).
  • CIP cold isostatic pressing
  • the compact thus obtained is sintered at a temperature equal to or higher than the liquid phase appearance temperature in vacuum or in an inert atmosphere.
  • the liquefaction start temperature of the compact is the temperature at which the liquefaction starts during the heating process of sintering, and is measured using a differential thermal analyzer.
  • the upper limit of the sintering temperature is preferably liquid phase appearance temperature + 100°C.
  • the obtained sintered body may be further subjected to HIP treatment.
  • the cemented carbide of the present invention is used for punches, crimping punches and dies for motor core materials, punches and dies for lead frame materials, slitters, powder molding dies, drawing punches and dies, drawing dies, nozzles, rotary blades, etc. be able to.
  • the cemented carbide of the present invention has excellent wear resistance and fracture toughness, good chipping resistance, and excellent adhesion resistance.
  • it can be suitably used as punches, caulking punches, drawing punches, and dies for metal motor core materials, lead frame materials, and the like.
  • cemented carbide of the present invention will be specifically described below, the present invention is not limited to this and can be appropriately modified within the scope of the technical idea.
  • Example 2 As raw material powders, coarse-grained WC powder, fine-grained WC powder with different particle sizes, Co powder (1.4 ⁇ m), Ni powder (2.4 ⁇ m), and Cr 3 C 2 powder (2.4 ⁇ m) were used. Table 1 shows the average grain size of coarse WC and fine WC. The average particle size was measured by the FSSS method. Using these powders, powders having the composition shown in Table 1 were blended, wet-mixed and pulverized, and dried to obtain a mixed powder. After pressure-molding this mixed powder, vacuum sintering was performed at 1400° C. to produce a cemented carbide.
  • FIG. 1 shows the relationship between the amount of Co added and the average particle size of WC fine particles.
  • Example 8 SEM photographs (observation magnification: 2000 times) showing the polished cross sections of Example 8 and Comparative Example 9 are shown in FIGS. 2(a) and 2(b).
  • the dark-colored binder phase particles surrounded by the light-colored WC particles are each small, and there is only one thick part of the binder phase with a diameter of 2.5 ⁇ m or more and less than 4.0 ⁇ m when the area is converted to a circle. observed.
  • the sample structure of Comparative Example 9 several thick portions of the binder phase were observed, and four thick portions of the binder phase with a diameter of 2.5 ⁇ m or more and less than 4.0 ⁇ m and one with a diameter of 4.0 ⁇ m or more were confirmed.
  • the Vickers hardness is measured using a Vickers hardness tester HV30
  • the transverse rupture strength is measured by a three-point bending test based on JISR 1601
  • the fracture toughness value K IC is the crack length generated at the Vickers indentation corner based on JIS R 1607.
  • the number of binder phases was calculated by converting the diameter of a circle having the same area by image analysis from an SEM photograph (observation magnification: 600 times) showing a polished cross section of the cemented carbide. Table 3 shows the results obtained.
  • a punching test was performed on the cemented carbides of Examples 1 to 9 and Comparative Examples 1 to 11. Punching tests were performed on a steel plate (round punch tip diameter 3.0 mm, processed material SPCC thin plate 0.5 mm thick, clearance 0.03 mm, punching speed 300 shots/min, 1.2 million shots). and the amount of adhesion of the work material.
  • Comparative Example 7 is a material similar to the existing mold material, but if compared to Comparative Example 7, the amount of wear, chipping, and the amount of adhesion of the work material are improved, ⁇ , and if it is particularly excellent, ⁇ , If it is equivalent, it is evaluated as ⁇ , and if it is inferior, it is evaluated as ⁇ .
  • the above punching test results were comprehensively evaluated, and the tool was evaluated as ⁇ if it was excellent as a tool, ⁇ if it was particularly excellent, and ⁇ if it was not sufficient. Table 4 shows the results obtained.
  • the cemented carbides of Examples 1, 4, and 8 had good hardness, transverse rupture strength, and the number of thick portions of the binder phase, and also had excellent fracture toughness. improved chipping.
  • the cemented carbides of Examples 2, 5 and 9 have a slightly larger number of thick portions of the binder phase, but this is not so bad as to adversely affect the actual punching test, and the fracture toughness is also high, so that the punching test gives good results.
  • the cemented carbides of Examples 3 and 7 had the same fracture toughness as Comparative Example 7, but the number of thick portions of the binder phase was very small, and the chipping in the punch test was the same as that of Comparative Example 7. The amount of wear and the amount of adhesion were very good.
  • the cemented carbide of Example 6 is one in which part of Co in the composition of Example 5 is replaced with Ni. It was expected to show excellent performance when used in a corrosive environment without adversely affecting the environment.
  • the area ratio of WC coarse particles to the total WC was as high as 73 and 83 area%, and the amount of Co added was as very small as 6 mass%, so the transverse rupture strength and fracture toughness was inferior and chipping increased.
  • the area ratio of WC coarse particles to the total WC is as high as 71 and 86 area%, and the number of thick portions of the binder phase is very large, resulting in adhesive wear and machining. Chipping increased due to increased load.
  • the cemented carbides of Comparative Examples 5 and 8 since the average grain size of the WC fine particles was small relative to the amount of Co added, the hardness was high and the toughness was insufficient, resulting in increased chipping.
  • the cemented carbides of Comparative Examples 6 and 9 since the average grain size of the WC fine particles is large relative to the amount of Co added, the toughness is high, but there are many thick portions of the binder phase, and adhesion and wear occur. .
  • the cemented carbide of Comparative Example 7 has a small average grain size of the WC coarse particles and a low area ratio of the WC coarse particles to the total WC, so that the fracture toughness is inferior and the chipping resistance is insufficient.
  • the cemented carbides of Comparative Examples 10 and 11 which had a large Co content of 16% by mass, were inferior in hardness and had an increased number of thick portions of the binder phase, resulting in adhesion and wear.
  • the content X of the binder phase is 10 to 15 mass% of the entire cemented carbide
  • the area ratio of the WC coarse particles is 20 to 35 area% of the entire WC
  • the average of the WC coarse particles is The average particle diameter Y of WC fine particles is contained in the range of 2 ⁇ m or more and less than 4 ⁇ m, and the following formula (1) -0.065X + 1.20 ⁇ Y ⁇ -0.065X + 1.70 (1)

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)
  • Powder Metallurgy (AREA)

Abstract

Un alliage extra-dur comprend une phase dure avec WC en tant que composant principal et une phase de liaison avec Co en tant que composant principal, la phase dure comprenant des particules de WC grossières ayant une taille de particule supérieure ou égale à 1,6 à moins de 6,0 µm et de fines particules de WC ayant une taille de particule inférieure à 1,6 µm, le rapport de surface des particules de WC grossières étant de 20 à 35 % en surface du WC total, le rapport de surface des fines particules de WC étant de 65 à 80 % en surface du WC total, la teneur X de la phase de liaison étant de 10 à 15 % en masse de l'ensemble de l'alliage extra-dur, la taille moyenne de particule des particules de WC grossières étant dans la plage de 2 µm ou plus et inférieure à 4 µm, et la taille de particule moyenne Y des fines particules de WC satisfaisant la formule suivante (1) : -0,065X + 1,20 ≤ Y ≤ -0,065X + 1,70.
PCT/JP2021/013918 2021-03-31 2021-03-31 Alliage extra-dur et moule Ceased WO2022208766A1 (fr)

Priority Applications (2)

Application Number Priority Date Filing Date Title
JP2021518023A JP6900099B1 (ja) 2021-03-31 2021-03-31 超硬合金及び金型
PCT/JP2021/013918 WO2022208766A1 (fr) 2021-03-31 2021-03-31 Alliage extra-dur et moule

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
PCT/JP2021/013918 WO2022208766A1 (fr) 2021-03-31 2021-03-31 Alliage extra-dur et moule

Publications (1)

Publication Number Publication Date
WO2022208766A1 true WO2022208766A1 (fr) 2022-10-06

Family

ID=76649970

Family Applications (1)

Application Number Title Priority Date Filing Date
PCT/JP2021/013918 Ceased WO2022208766A1 (fr) 2021-03-31 2021-03-31 Alliage extra-dur et moule

Country Status (2)

Country Link
JP (1) JP6900099B1 (fr)
WO (1) WO2022208766A1 (fr)

Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07252579A (ja) * 1994-03-11 1995-10-03 Sumitomo Electric Ind Ltd 切削工具用の被覆超硬合金
JP2004330314A (ja) * 2003-04-30 2004-11-25 Sumitomo Electric Ind Ltd 被覆超硬合金工具
WO2018180911A1 (fr) * 2017-03-30 2018-10-04 京セラ株式会社 Plaquette de coupe et outil de coupe

Patent Citations (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH07252579A (ja) * 1994-03-11 1995-10-03 Sumitomo Electric Ind Ltd 切削工具用の被覆超硬合金
JP2004330314A (ja) * 2003-04-30 2004-11-25 Sumitomo Electric Ind Ltd 被覆超硬合金工具
WO2018180911A1 (fr) * 2017-03-30 2018-10-04 京セラ株式会社 Plaquette de coupe et outil de coupe

Also Published As

Publication number Publication date
JP6900099B1 (ja) 2021-07-07
JPWO2022208766A1 (fr) 2022-10-06

Similar Documents

Publication Publication Date Title
KR102441723B1 (ko) 서멧, 절삭 공구, 및 서멧의 제조 방법
JP5152770B1 (ja) 強靭超硬合金の製造方法
JP2004076049A (ja) 超微粒超硬合金
JP5856752B2 (ja) 炭化タングステン基焼結体およびそれを用いた耐摩耗部材
JP2004059946A (ja) 超微粒超硬合金
JP6922110B1 (ja) 粉砕・撹拌・混合・混練機部材
EP3950183B1 (fr) Outil de coupe en carbure cémenté à base de wc présentant une excellente résistance aux défauts et une excellente résistance à l'ébréchure et outil de coupe en carbure cémenté à base de wc revêtu en surface
JP2020094277A (ja) Ｗｃ基超硬合金およびこれを用いた被覆切削工具
JP2017148895A (ja) 耐折損性にすぐれたｗｃ基超硬合金製ドリル
JP7599607B1 (ja) モリブデン複合材料およびそれを用いたモリブデン複合材料成形品並びにモリブデン複合材料の製造方法
WO2022208766A1 (fr) Alliage extra-dur et moule
JP2007162066A (ja) 微粒超硬合金及び希土類元素含有微粒超硬合金の製造方法
JP6695566B2 (ja) 非金属系材料を加工するための工具に用いる超硬合金
JP2020132935A (ja) 耐欠損性にすぐれたｗｃ基超硬合金製切削工具および表面被覆ｗｃ基超硬合金製切削工具
JP5826138B2 (ja) 強靱超硬合金及び被覆超硬合金
JP4126280B2 (ja) 微粒超硬合金
JP7473871B2 (ja) 耐摩耗性および耐欠損性にすぐれたｗｃ基超硬合金製切削工具および表面被覆ｗｃ基超硬合金製切削工具
JP4776395B2 (ja) 切削工具
JP2007191741A (ja) Ｗｃ基超硬合金及びその製造方法
JP7508155B1 (ja) 軽量硬質合金の製造方法
JP7293787B2 (ja) ＴａＷＳｉターゲットおよびその製造方法
JPH10324943A (ja) 微粒超硬合金及びその製造方法
JP2012512963A (ja) サーメット
JP2004052110A (ja) 超微粒超硬合金
WO2021039712A1 (fr) Cible à base de ｆｅ－ｓｉ－ｂ－ｎｂ

Legal Events

Date Code Title Description
ENP Entry into the national phase

Ref document number: 2021518023

Country of ref document: JP

Kind code of ref document: A

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

Ref document number: 21934932

Country of ref document: EP

Kind code of ref document: A1

NENP Non-entry into the national phase

Ref country code: DE

122 Ep: pct application non-entry in european phase

Ref document number: 21934932

Country of ref document: EP

Kind code of ref document: A1