WO2018198414A1 - Outil de coupe - Google Patents

Outil de coupe Download PDF

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Publication number
WO2018198414A1
WO2018198414A1 PCT/JP2017/042850 JP2017042850W WO2018198414A1 WO 2018198414 A1 WO2018198414 A1 WO 2018198414A1 JP 2017042850 W JP2017042850 W JP 2017042850W WO 2018198414 A1 WO2018198414 A1 WO 2018198414A1
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WO
WIPO (PCT)
Prior art keywords
sintered body
less
cutting tool
phase
tool according
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PCT/JP2017/042850
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English (en)
Japanese (ja)
Inventor
博香 青山
慶春 内海
裕明 後藤
津田　圭一
Original Assignee
住友電気工業株式会社
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.)
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Application filed by 住友電気工業株式会社 filed Critical 住友電気工業株式会社
Priority to PCT/JP2018/014693 priority Critical patent/WO2018198719A1/fr
Priority to JP2019514341A priority patent/JP7143844B2/ja
Priority to TW107113484A priority patent/TW201843312A/zh
Publication of WO2018198414A1 publication Critical patent/WO2018198414A1/fr

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B27/00—Tools for turning or boring machines; Tools of a similar kind in general; Accessories therefor
    • B23B27/14—Cutting tools of which the bits or tips or cutting inserts are of special material
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23B—TURNING; BORING
    • B23B51/00—Tools for drilling machines
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23C—MILLING
    • B23C5/00—Milling-cutters
    • B23C5/16—Milling-cutters characterised by physical features other than shape
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/04—Making non-ferrous alloys by powder metallurgy
    • C22C1/05—Mixtures of metal powder with non-metallic powder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C19/00—Alloys based on nickel or cobalt
    • 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 cutting tool.
  • This application claims priority based on Japanese Patent Application No. 2017-0868857, which is a Japanese patent application filed on April 26, 2017. All the descriptions described in the Japanese patent application are incorporated herein by reference.
  • cutting tools are products that require high hardness.
  • hard materials sintered bodies
  • cemented carbide, cermet and the like are known.
  • Patent Document 1 Japanese Patent Laid-Open No. 9-125229
  • Patent Document 2 Japanese Patent Laid-Open No. 2014-208889 discloses a sintered body including hard particles made of WC and a metal phase represented by (Co, Ni) 3 (Al, W, V, Ti). It is disclosed.
  • Cutting tool includes a sintered body containing the first hard phase, a binder phase and Al 2 O 3.
  • the first hard phase is composed of WC particles.
  • the binder phase includes at least one first metal selected from Co and Ni as a main component, and further includes C and at least one second metal selected from Al and W.
  • Al 2 O 3 is dispersed in the sintered body.
  • FIG. 1 is a reference diagram related to the evaluation of a cutting tool.
  • an object of the present disclosure is to provide a cutting tool with improved wear resistance at high temperatures.
  • the notation in the form of “A to B” means the upper and lower limits of the range (that is, A or more and B or less), and the unit is not described in A but only the unit B is described The unit of A and the unit of B are the same.
  • a cutting tool includes a sintered body including a first hard phase, a binder phase, and Al 2 O 3 .
  • the first hard phase is composed of WC particles.
  • the binder phase includes at least one first metal selected from Co and Ni as a main component, and further includes C and at least one second metal selected from Al and W.
  • Al 2 O 3 is in the form of particles and is dispersed in the sintered body.
  • the sintered body has improved wear resistance at high temperatures. By improving the wear resistance of the sintered body at a high temperature, it is possible to extend the life of the cutting tool.
  • the binder phase preferably includes a compound phase represented by the following formula. (Co, Ni) x (Al, W) y C z [Wherein (Co, Ni) is at least one selected from Co and Ni, (Al, W) is at least one selected from Al and W, and x, y, and z are atomic weight ratios. It is. This makes it possible for the sintered body to maintain high hardness, particularly at high temperatures.
  • x is 0.6 or more and 0.95 or less
  • y is 0.04 or more and 0.32 or less
  • z is 0.003 or more and 0.15 or less. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • x is preferably 0.75 or more and 0.93 or less
  • y is 0.05 or more and 0.2 or less
  • z is preferably 0.005 or more and 0.1 or less. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • x is preferably 0.8 to 0.9
  • y is preferably 0.06 to 0.12
  • z is preferably 0.01 to 0.05. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • the sintered body further includes a second hard phase.
  • the second hard phase is one or more metals selected from the group consisting of Ti, Zr, Hf, Nb, Ta, Cr, Mo and W, and one or more selected from the group consisting of nitrogen, carbon, boron and oxygen Or a solid solution of the compound (excluding WC).
  • the volume ratio of the first hard phase is larger than that of the second hard phase. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • Al 2 O 3 is preferably contained in the sintered body in an amount of 1% by volume to 15% by volume. In this case, the effect of improving the wear resistance at high temperatures can be obtained more reliably, and the effect of suppressing the decrease in the strength of the sintered body is expected.
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.1 ⁇ m to 2 ⁇ m, and a standard deviation of 0.05 ⁇ m to 0.25 ⁇ m. In this case, an effect of improving the hardness of the sintered body is expected. Moreover, the effect that the fall of the toughness of a sintered compact is suppressed is anticipated.
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.2 ⁇ m to 1 ⁇ m and a standard deviation of 0.05 ⁇ m to 0.15 ⁇ m. In this case, the effect of further improving the hardness of the sintered body is expected. Moreover, the effect that the fall of the toughness of a sintered compact is suppressed is anticipated.
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.3 ⁇ m or more and 0.5 ⁇ m or less and a standard deviation of 0.05 ⁇ m or more and 0.1 ⁇ m or less. In this case, the effect of further improving the hardness of the sintered body is expected. Moreover, the effect that the fall of the toughness of a sintered compact is suppressed is anticipated.
  • Al 2 O 3 preferably has an average interparticle distance of 1 ⁇ m to 3 ⁇ m, and a standard deviation of 0.5 ⁇ m to 1.5 ⁇ m. In this case, the effect of maintaining the hardness toughness balance is expected.
  • the ratio of the mass of O to the mass of C contained in the sintered body is preferably 0.015 or more and 0.061 or less. In this case, it is expected to satisfy [8] and [11].
  • the oxygen content in the sintered body is preferably 0.1% by mass or more and 0.4% by mass or less. In this case, an effect of improving the hardness of the sintered body and an effect of suppressing defects are expected.
  • the binder phase preferably has a lattice constant of 3.65 to 4.0 mm. In this case, an effect of maintaining the high hardness of the sintered body at a higher temperature and an effect of suppressing defects of the sintered body are expected.
  • the WC particles preferably have an average particle diameter of 0.1 ⁇ m to 3 ⁇ m. In this case, the effect which suppresses the defect
  • the binder phase content in the sintered body is preferably 2% by mass or more and less than 10% by mass. In this case, the effect which suppresses the defect
  • the present embodiment includes any conventionally known atomic ratio, and is not necessarily limited to a stoichiometric range.
  • the cutting tool according to the present embodiment includes the following sintered body.
  • Cutting tools include drills, end mills, drill tip changeable cutting tips, end mill tip replacement cutting tips, milling tip replacement cutting tips, turning tip replacement cutting tips, metal saws, and cutting tools. , Reamers, taps and the like.
  • the sintered body according to the present embodiment includes a first hard phase, a binder phase, and Al 2 O 3 .
  • the sintered body may contain components other than these as long as these are included.
  • the first hard phase is composed of WC particles.
  • the first hard phase is composed of an aggregate of a plurality of particles, and the binder phase is scattered as particles in the first hard phase.
  • Al 2 O 3 is in the form of particles and is dispersed in the sintered body.
  • the binder phase contains at least one first metal selected from Co and Ni as a main component, and further contains at least one second metal selected from Al and W, and C.
  • the “main component” means a component having the largest blending ratio (mass%) among the components constituting the binder phase.
  • the sintered body contains C in the binder phase. For this reason, the high temperature hardness of the binder phase is improved by solid solution strengthening, so that the wear resistance of the sintered body at a high temperature is improved.
  • the binder phase is composed of a heat-resistant alloy (Co-base superalloy, Ni-base superalloy, etc.) instead of metallic Co.
  • a heat-resistant alloy is a material used for components used at high temperatures such as jet engines and gas turbines, and is excellent in heat resistance at high temperatures.
  • the sintered body contains Al 2 O 3 having a hardness higher than that of WC. As a result, the hardness of the sintered body itself is improved.
  • the first hard phase and the binder phase are preferably contained in a state dispersed in the sintered body. This improves the wear resistance of the sintered body at a high temperature. Moreover, it is preferable that both the first hard phase and the binder phase are contained in a state of being dispersed in the sintered body together with the ⁇ phase that is a matrix phase made of the first metal (Co, Ni). Thereby, the sintered compact which made high temperature hardness and defect resistance compatible can be obtained. It is more preferable that both are contained in a uniformly dispersed state in the sintered body.
  • the dispersed state means that the first hard phase and the binder phase are in contact with each other and the presence of the same kind of phases in the sintered body is relatively small.
  • the binder phase preferably contains a compound phase represented by the following formula. (Co, Ni) x (Al, W) y C z [Wherein (Co, Ni) is at least one selected from Co and Ni, (Al, W) is at least one selected from Al and W, and x, y, and z are atomic weight ratios. It is. ] Note that oxygen may be contained (solid solution) in the binder phase.
  • Such a sintered body contains (Co, Ni) x (Al, in the matrix phase ( ⁇ phase) composed of the first metal (Co, Ni) and the second metal (Al, W)) in the binder phase.
  • W by including a compound phase represented by y C z, the sintered body, it is possible to particularly maintaining high hardness at elevated temperatures.
  • X is preferably 0.6 or more and 0.95 or less
  • y is 0.04 or more and 0.32 or less
  • z is preferably 0.003 or more and 0.15 or less. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • X is preferably 0.75 or more and 0.93 or less
  • y is 0.05 or more and 0.2 or less
  • z is preferably 0.005 or more and 0.1 or less. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • X is preferably 0.8 or more and 0.9 or less
  • y is 0.06 or more and 0.12 or less
  • z is 0.01 or more and 0.05 or less. This is because an improvement in wear resistance at high temperatures of the sintered body is expected.
  • the sintered body preferably further includes a second hard phase.
  • the second hard phase is one or more metals selected from the group consisting of Ti, Zr, Hf, Nb, Ta, Cr, Mo and W, and one or more selected from the group consisting of nitrogen, carbon, boron and oxygen Or a solid solution of the compound (excluding WC).
  • the volume ratio of the first hard phase is larger than that of the second hard phase.
  • the binder phase Since the binder phase has a higher affinity for the first hard phase than the second hard phase, the volume ratio of the first hard phase is larger than that of the second hard phase. This is expected to improve the wear resistance of sintered bodies at high temperatures.
  • Al 2 O 3 is preferably contained in the sintered body in an amount of 1% by volume to 15% by volume. If the amount of Al 2 O 3 is too small, the effect of improving the wear resistance at high temperatures may not be obtained. On the other hand, if the amount of Al 2 O 3 is too large, the strength of the sintered body is likely to occur is reduced defects. For this reason, when the content ratio of Al 2 O 3 is in the above range, the effect of improving the wear resistance at high temperatures can be obtained more reliably, and the effect of suppressing the decrease in the strength of the sintered body is expected. .
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.1 ⁇ m to 2 ⁇ m and a standard deviation of 0.05 ⁇ m to 0.25 ⁇ m. Since Al 2 O 3 is fine, an effect of further improving the hardness of the sintered body is expected. On the other hand, if Al 2 O 3 is too fine, the toughness of the sintered body is lowered and defects are likely to occur, so that an effect of suppressing the toughness of the sintered body from being suppressed in the above range is expected.
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.2 ⁇ m or more and 1 ⁇ m or less, and a standard deviation of 0.05 ⁇ m or more and 0.15 ⁇ m or less. Since Al 2 O 3 is fine, an effect of further improving the hardness of the sintered body is expected. On the other hand, if Al 2 O 3 is too fine, the toughness of the sintered body is lowered and defects are likely to occur, so that an effect of suppressing the toughness of the sintered body from being suppressed in the above range is expected.
  • Al 2 O 3 preferably has an average equivalent circle diameter of 0.3 ⁇ m or more and 0.5 ⁇ m or less, and a standard deviation of 0.05 ⁇ m or more and 0.1 ⁇ m or less. Since Al 2 O 3 is fine, an effect of further improving the hardness of the sintered body is expected. On the other hand, if Al 2 O 3 is too fine, the toughness of the sintered body is lowered and defects are likely to occur, so that an effect of suppressing the toughness of the sintered body from being suppressed in the above range is expected.
  • Al 2 O 3 preferably has an average interparticle distance of 1 ⁇ m to 3 ⁇ m and a standard deviation of 0.5 ⁇ m to 1.5 ⁇ m. Since the binder phase is uniformly dispersed, an effect of maintaining the hardness-toughness balance is expected. When the distance between the particles deviates from 1 to 3 ⁇ m, the degree of dispersion of the binder phase is biased and defects are likely to occur.
  • the interparticle distance is set to one for each Al 2 O 3 particle. "Interparticle distance" in any one of Al 2 O 3 particles, the distance between the center of gravity of the Al 2 O 3 particles, and other Al 2 O 3 particles having a center of gravity to the position nearest the heavy center point It is.
  • the “average value of interparticle distance” is an average value of all “interparticle distances”.
  • the ratio of the mass of O to the mass of C contained in the sintered body is preferably 0.015 or more and 0.061 or less. Within this range, Al 2 O 3 is expected to uniformly disperse and precipitate to satisfy [8] and [11].
  • the oxygen content in the sintered body is preferably 0.1% by mass or more and 0.4% by mass or less. If the oxygen content is 0.1% by mass or less, Al 2 O 3 may not precipitate and the hardness may not be improved. If the oxygen content is 0.4% by mass or more, Al 2 O 3 aggregates and defects may easily occur. For this reason, when the oxygen content is in the above range, an effect of improving the hardness of the sintered body and an effect of suppressing defects are expected.
  • the binder phase preferably has a lattice constant of 3.65 to 4.0 mm.
  • the lattice constant of the binder phase is 3.65% or more, C dissolves and distortion occurs, so that high hardness can be maintained at higher temperatures.
  • the lattice constant of the binder phase is larger than 4.0%, the strain becomes large, and cracks may occur in the binder phase to cause defects. For this reason, when the lattice constant of the binder phase is in the above range, an effect of maintaining a high hardness of the sintered body at a higher temperature and an effect of suppressing defects of the sintered body are expected.
  • WC particles preferably have an average particle size of 0.1 ⁇ m or more and 3 ⁇ m or less.
  • the average particle size is 0.1 ⁇ m or less, the toughness of the sintered body may be reduced and defects may occur.
  • the average particle diameter is 5 ⁇ m or more, the strength of the sintered body is lowered, and there is a possibility that defects are likely to occur. For this reason, when the average particle diameter of WC particle
  • the binder phase content in the sintered body is preferably 2% by mass or more and less than 10% by mass.
  • the toughness of the sintered body may be reduced and defects may be easily generated.
  • the content of the binder phase is more than 10% by mass, the high temperature hardness of the sintered body may be easily lowered. For this reason, when the content rate of a binder phase exists in said range, the effect which suppresses the defect
  • the sintered body contains a hard phase (first hard phase and second hard phase), a binder phase (alloy powder) and Al 2 O 3 , and a hard phase (first hard phase and second hard phase). ),
  • the volume content of the binder phase or Al 2 O 3 , the average particle diameter of the WC particles (first hard phase), the equivalent circle diameter or interparticle distance of Al 2 O 3 , the composition of the binder phase, etc. It can be confirmed as follows.
  • a sample including an arbitrary cross section of the sintered body is prepared.
  • a focused ion beam device, a cross section polisher device, or the like can be used.
  • the processed cross section is imaged at a magnification of 10,000 with an SEM (Scanning Electron Microscope) to obtain an electronic image for 10 fields of view.
  • element mapping is performed on a predetermined region (12 ⁇ m ⁇ 9 ⁇ m) in each electronic image by using attached EPMA (Electron Probe Micro-Analysis) or EDX (Energy Dispersive X-ray spectroscopy).
  • the region containing WC is the first hard phase, the region does not contain WC, and includes the first metal (Ni, Co), the second metal (Al, W), and C.
  • a region is a binder phase, and a region containing Al and O is Al 2 O 3 .
  • the sintered body is hard phase (first hard phase and the second hard phase), it is confirmed that contains a binding phase and Al 2 O 3.
  • the composition of the binder phase and the ratio (volume%) of the binder phase in the sintered body are determined. Depending on the sintering conditions, pores may exist in addition to the hard phase and the binder phase.
  • composition of the compound particles constituting the hard phase (the first hard phase and the second hard phase), and the respective proportions (mass%) of the WC particles (first hard phase) and the compound particles are obtained by crushing the sintered body.
  • the content ratio of each element in the pulverized product can be obtained by ICP emission spectroscopic analysis, and the composition ratio of each component can be estimated based on this.
  • the content ratio of the WC particles in the sintered body is relatively high. For this reason, there are many regions where the WC particles are adjacent to each other. Adjacent WC particles can be distinguished from each other by the result of elemental mapping and the reflected electron image obtained from the SEM image. This is because in the reflected electron image, a color difference (light / dark) due to a difference in crystal orientation of each WC particle is observed.
  • first, the first metal (Co, Ni) and the second metal (Al, W) are used as raw materials, and a bonded phase is produced by atomization, arc melting, plasma treatment, or the like.
  • V, Ti, Nb, Ta, B, C, etc. may be added in addition to the first metal (Co, Ni) and the second metal (Al, W). .
  • the obtained binder phase is pulverized by, for example, a bead mill, a ball mill, a jet mill or the like to become a binder phase powder.
  • the average particle size of the binder phase powder is preferably 0.3 to 3 ⁇ m.
  • the beads / balls used in the bead mill / ball mill include beads / balls made of alumina, silicon nitride, and cemented carbide having a particle diameter of 0.1 to 3 mm.
  • the dispersion medium include ethanol, acetone, and liquid nitrogen. Is mentioned.
  • the processing time by the bead mill / ball mill is, for example, 30 minutes to 200 hours.
  • the slurry obtained by the bead mill / ball mill is dried, for example, in the atmosphere.
  • a binder phase powder having oxygen adsorbed can be obtained by using air as a pulverization gas source and taking a long pulverization time.
  • a sintered body in which Al 2 O 3 is dispersed can also be obtained by directly adding Al 2 O 3 powder, but it is more preferable to deposit Al 2 O 3 as in this method.
  • the particle size of Al 2 O 3 can be reduced, which is preferable.
  • the obtained binder phase powder and the separately prepared WC particle powder are mixed by an attritor, ball mill, mortar or the like. At this time, appropriate C is added in consideration of the amount of C contained in the binder phase.
  • the mixing time is preferably 6 to 20 hours so that oxygen is sufficiently and uniformly incorporated into the mixture.
  • Examples of the balls used in the ball mill include balls made of alumina, silicon nitride, or cemented carbide and having a diameter of 3 mm.
  • Examples of the dispersion medium include ethanol, acetone, and liquid nitrogen.
  • the processing time is, for example, 3 to 20 hours.
  • the mixed powder is obtained by drying the slurry obtained by mixing, for example, in the air. Upon mixing, the Al 2 O 3 dispersed in the sintered body Al 2 O 3 may be added to the powder (0.01 ⁇ 0.5 ⁇ m).
  • the obtained mixed powder is placed in, for example, a cemented carbide mold (Ta capsule or the like) and pressed to obtain a pressure-formed body.
  • the pressure of the press is preferably 10 MPa to 16 GPa, for example, 100 MPa.
  • the pressure-molded body is sintered in a vacuum.
  • the sintering temperature is preferably 1000 to 1800 ° C.
  • the sintering time is, for example, about 1 hour.
  • the keep time at 400 ° C. is set to 30 minutes to 5 hours to desorb C contained in the molded body, and finally the mass of C contained in the sintered body. Control is performed so that the ratio of the mass of O to (C / O ratio) becomes a desired value.
  • the first hard phase (WC particles) and the binder phase are densely sintered, and fine Al 2 O 3 is precipitated in the sintered body, thereby improving the wear resistance at high temperature.
  • the body can be formed.
  • the cooling rate after sintering is set to 2 to 20 ° C./min, for example.
  • the compound phase represented by the following formula precipitates.
  • (Co, Ni) x (Al, W) y C z [Wherein (Co, Ni) is the first metal, (Al, W) is the second metal, and x, y and z are atomic weight ratios. ]
  • a hot isostatic pressing (HIP) process is performed at 1400 ° C. and 1000 atm for 1 hour to obtain a sintered body (alloy).
  • the average particle diameter of WC particles is preferably 0.1 to 10 ⁇ m, and the content of WC particles in the sintered body (hard material) is preferably 50 to 99% by volume. This is because the hardness of the obtained sintered body is expected to be higher when the particle size range and the composition range are in this range.
  • grains can be measured by the method using the above-mentioned element mapping and image analysis software.
  • the sintered body of the present embodiment may contain inevitable impurities (B, N, O, etc.) within a range that does not impair the effects of the present disclosure.
  • the sintered body of the present embodiment may include an abnormal layer called free carbon or ⁇ phase in the structure.
  • Examples 1 to 50 Metal powder was mixed with a composition of 42.5Co-40Ni-10W-7.5Al (atomic%), and a binder phase was prepared by an atomizing method. (All metal powders used in Examples 1 to 50 are the same.) The obtained binder phase was pulverized by a bead mill using superhard balls having a particle diameter of 1 ⁇ m. The obtained slurry was dried in the air to obtain a binder phase powder.
  • the mixture was put into an open atmosphere attritor and mixed.
  • the mixing time of the attritor is as shown in Tables 1 and 2.
  • the obtained slurry was dried in the air to obtain a mixed powder.
  • the mixed powder was filled in a cemented carbide mold and pressed at a pressure of 100 MPa to obtain a pressure-formed body.
  • This press-molded body was sintered at 1450 ° C. for 1 hour under the sintering conditions described in Tables 1 and 2. At this time, by setting the keep time at 400 ° C. in a hydrogen atmosphere as shown in Table 1 and Table 2, C contained in the molded body is desorbed, and finally the C / O ratio contained in the sintered body is set. Control was performed as shown in Tables 3 and 4. Further, the cooling rate was adjusted as described in Tables 1 and 2. Thereby, (Co, Ni) x ( Al, W) y compound phase represented by C z precipitated.
  • a sintered body (hard material) was obtained by performing hot isostatic pressing (HIP) processing at 1400 ° C. under the condition of 1000 atm for 1 hour.
  • HIP hot isostatic pressing
  • the sintered body includes a hard phase (first hard phase and second hard phase), a binder phase (alloy powder) and Al 2 O 3 , and a hard phase (first hard phase and second hard phase);
  • the volume content of the binder phase or Al 2 O 3 , the composition of the binder phase, and the like were measured in the same manner as the method described in the above embodiment.
  • the amount of oxygen and the amount of C in the sintered body were measured by ICP emission spectroscopic analysis after pulverizing the sintered body.
  • the lattice constant of the binder phase was specified by EDS analysis and an electron beam diffraction image in a limited field of view of TEM observation.
  • JEM-2100F / Cs manufactured by JEOL Ltd.
  • Cs collector CESCOR (manufactured by CEOS) was used.
  • CEOS CEOS
  • EDS machine a JED2300 Series dry SD60GV detector (manufactured by JEOL Ltd.) was used.
  • the TEM observation conditions were acceleration voltage: 200 kV and probe size: 0.13 nm.
  • Boundary wear is a portion where wear increases due to strength reduction, chipping or particle dropout.
  • the binder phase is of the formula: (Co, Ni) x (Al, W) y C z [Wherein (Co, Ni) is the first metal, (Al, W) is the second metal, and x, y and z are atomic weight ratios. ] And x is 60 atomic% or more and 95 atomic% or less, y is 4 atomic% or more and 32 atomic% or less, and z is 0.3 atomic% or more and 15 atomic% or less. When it is below, it turns out that the abrasion resistance in high temperature is improving more.

Abstract

L'invention concerne un outil de coupe contenant un corps fritté qui comporte une première phase dure, une phase liante et Al2O3. La première phase dure comprend des particules de WC. La phase liante contient un premier métal comprenant au moins un élément choisi parmi Co et Ni en tant que constituants principaux, et contient en outre C et un second métal comprenant au moins un élément choisi parmi Al et W. Al2O3 est particulaire et est dispersé dans le corps fritté.
PCT/JP2017/042850 2017-04-26 2017-11-29 Outil de coupe WO2018198414A1 (fr)

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Application Number Priority Date Filing Date Title
PCT/JP2018/014693 WO2018198719A1 (fr) 2017-04-26 2018-04-06 Outil de coupe
JP2019514341A JP7143844B2 (ja) 2017-04-26 2018-04-06 切削工具
TW107113484A TW201843312A (zh) 2017-04-26 2018-04-20 切削工具

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JP2017-086857 2017-04-26
JP2017086857 2017-04-26

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PCT/JP2018/014693 WO2018198719A1 (fr) 2017-04-26 2018-04-06 Outil de coupe

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Citations (6)

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JPS61235533A (ja) * 1985-04-08 1986-10-20 Sumitomo Electric Ind Ltd 高耐熱性超硬合金
JPH11124650A (ja) * 1997-10-20 1999-05-11 Toshiba Tungaloy Co Ltd 酸化物により粒内分散強化されたｗｃ含有超硬合金およびその製法
JP2000219931A (ja) * 1999-01-29 2000-08-08 Seco Tools Ab 超硬合金及びその製造方法
JP2005213525A (ja) * 2004-01-27 2005-08-11 Tungaloy Corp 複合酸化物分散焼結合金
JP2005336565A (ja) * 2004-05-27 2005-12-08 Kyocera Corp 超硬合金
JP2011098875A (ja) * 2009-11-09 2011-05-19 Sumitomo Electric Ind Ltd 立方晶窒化硼素焼結体

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JP2001049378A (ja) 1999-06-03 2001-02-20 Ngk Spark Plug Co Ltd 耐摩耗性超硬合金焼結体及びその製造方法
JP5393004B2 (ja) 2007-06-27 2014-01-22 京セラ株式会社 超硬合金製小径棒状体および切削工具ならびにミニチュアドリル

Patent Citations (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS61235533A (ja) * 1985-04-08 1986-10-20 Sumitomo Electric Ind Ltd 高耐熱性超硬合金
JPH11124650A (ja) * 1997-10-20 1999-05-11 Toshiba Tungaloy Co Ltd 酸化物により粒内分散強化されたｗｃ含有超硬合金およびその製法
JP2000219931A (ja) * 1999-01-29 2000-08-08 Seco Tools Ab 超硬合金及びその製造方法
JP2005213525A (ja) * 2004-01-27 2005-08-11 Tungaloy Corp 複合酸化物分散焼結合金
JP2005336565A (ja) * 2004-05-27 2005-12-08 Kyocera Corp 超硬合金
JP2011098875A (ja) * 2009-11-09 2011-05-19 Sumitomo Electric Ind Ltd 立方晶窒化硼素焼結体

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TW201843312A (zh) 2018-12-16
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JP7143844B2 (ja) 2022-09-29

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