WO2014175419A1 - Objet fritté à base de nitrure de bore cubique et objet fritté revêtu à base de nitrure de bore cubique - Google Patents

Objet fritté à base de nitrure de bore cubique et objet fritté revêtu à base de nitrure de bore cubique Download PDF

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WO2014175419A1
WO2014175419A1 PCT/JP2014/061685 JP2014061685W WO2014175419A1 WO 2014175419 A1 WO2014175419 A1 WO 2014175419A1 JP 2014061685 W JP2014061685 W JP 2014061685W WO 2014175419 A1 WO2014175419 A1 WO 2014175419A1
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boron nitride
cubic boron
sintered body
nitride sintered
solid solution
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Japanese (ja)
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小林　幸太
香川　直宏
松原　秀彰
哲志 松田
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株式会社タンガロイ
一般財団法人ファインセラミックスセンター
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    • C04B35/00—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products
    • C04B35/515—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics
    • C04B35/58—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides
    • C04B35/583—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride
    • C04B35/5831—Shaped ceramic products characterised by their composition; Ceramics compositions; Processing powders of inorganic compounds preparatory to the manufacturing of ceramic products based on non-oxide ceramics based on borides, nitrides, i.e. nitrides, oxynitrides, carbonitrides or oxycarbonitrides or silicides based on boron nitride based on cubic boron nitrides or Wurtzitic boron nitrides, including crystal structure transformation of powder
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    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/38—Non-oxide ceramic constituents or additives
    • C04B2235/3852—Nitrides, e.g. oxynitrides, carbonitrides, oxycarbonitrides, lithium nitride, magnesium nitride
    • C04B2235/3856—Carbonitrides, e.g. titanium carbonitride, zirconium carbonitride
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C04B2235/30—Constituents and secondary phases not being of a fibrous nature
    • C04B2235/38—Non-oxide ceramic constituents or additives
    • C04B2235/3852—Nitrides, e.g. oxynitrides, carbonitrides, oxycarbonitrides, lithium nitride, magnesium nitride
    • C04B2235/3865—Aluminium nitrides
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
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    • C04B2235/40—Metallic constituents or additives not added as binding phase
    • C04B2235/402—Aluminium
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/02—Composition of constituents of the starting material or of secondary phases of the final product
    • C04B2235/50—Constituents or additives of the starting mixture chosen for their shape or used because of their shape or their physical appearance
    • C04B2235/54—Particle size related information
    • C04B2235/5418—Particle size related information expressed by the size of the particles or aggregates thereof
    • C04B2235/5436—Particle size related information expressed by the size of the particles or aggregates thereof micrometer sized, i.e. from 1 to 100 micron
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    • C04B2235/00—Aspects relating to ceramic starting mixtures or sintered ceramic products
    • C04B2235/70—Aspects relating to sintered or melt-casted ceramic products
    • C04B2235/74—Physical characteristics
    • C04B2235/76—Crystal structural characteristics, e.g. symmetry
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • C22C2026/003—Cubic boron nitrides only

Definitions

  • the present invention relates to a cubic boron nitride sintered body and a coated cubic boron nitride sintered body. Specifically, the present invention relates to a cubic boron nitride-containing sintered body and a coated cubic boron nitride sintered body that are optimal as cutting tools and wear-resistant tools.
  • Cubic boron nitride has characteristics that it has hardness next to diamond, excellent thermal conductivity, and low affinity with iron.
  • Cubic boron nitride sintered bodies made of cubic boron nitride and a binder phase of metal or ceramic have been applied to cutting tools, wear-resistant tools, and the like.
  • cubic boron nitride sintered bodies cubic boron nitride, aluminum oxide, aluminum nitride and / or aluminum boride, titanium carbide, titanium nitride and / or titanium carbonitride, titanium boride,
  • a cubic boron nitride sintered body made of for example, see Patent Document 1.
  • the present invention solves such a problem, and improves the fracture resistance and toughness without reducing the wear resistance, and increases the tool life of the cutting tool and the wear-resistant tool.
  • An object is to provide a coated cubic boron nitride sintered body.
  • the inventors have conducted research on a cubic boron nitride sintered body, and in order to increase the toughness of the cubic boron nitride sintered body, it is important to suppress propagation of the generated cracks, For this purpose, the inventors have obtained the knowledge that it is effective to have many grain boundaries in the binder phase of the cubic boron nitride sintered body, and have completed the present invention.
  • the present inventors have conducted research on a cubic boron nitride sintered body.
  • harder particles are used for forming a binder phase.
  • the present invention has been completed.
  • the gist of the present invention is as follows. (1) It consists of cubic boron nitride, a binder phase, and unavoidable impurities, and the binder phase is at least one element selected from the group consisting of Zr, Hf, V, Nb, Ta, Cr, Mo, and W.
  • a composite solid solution compound of Ti, the composite solid solution compound has a NaCl structure, and the half value of the (200) plane diffraction line of the composite solid solution compound obtained by X-ray diffraction measurement of 2 ⁇ / ⁇ method using Cu—K ⁇ rays
  • a cubic boron nitride sintered body having a width of 0.60 ° or more and 0.90 ° or less.
  • Atoms of Ti and M (wherein M represents at least one element selected from the group consisting of Zr, Hf, V, Nb, Ta, Cr, Mo and W) contained in the entire binder phase
  • the binder phase contains a composite solid solution compound, at least one aluminum compound selected from the group consisting of aluminum oxide, aluminum nitride and aluminum boride, and titanium boride (1) to (3) A cubic boron nitride sintered body according to any of the above.
  • the composite solid solution compound is (Ti 1-x M x ) (C 1-y N y ) (where x represents the atomic ratio of M to the total of Ti and M, and y represents the ratio of C and N (1) to (4) are composite solid solution compounds represented by the atomic ratio of N to the total, wherein x and y are 0.02 ⁇ x ⁇ 0.5 and 0 ⁇ y ⁇ 1, respectively. Any cubic boron nitride sintered body.
  • the cubic boron nitride sintered body has a cubic boron nitride: 10 to 90% by volume with respect to the entire cubic boron nitride sintered body, a binder phase and inevitable impurities: the entire cubic boron nitride sintered body.
  • the cubic boron nitride sintered body according to any one of (1) to (5) which is 10 to 90% by volume with respect to the total, and the total of these is 100% by volume.
  • the cubic boron nitride sintered body of the present invention comprises a binder phase, cubic boron nitride and unavoidable impurities.
  • the cubic boron nitride is less than 10% by volume with respect to the entire cubic boron nitride sintered body and the binder phase and inevitable impurities are more than 90% by volume with respect to the entire cubic boron nitride sintered body.
  • the deficiency is reduced, while the cubic boron nitride is more than 90% by volume with respect to the entire cubic boron nitride sintered body, and the binder phase is 10% by volume with respect to the entire cubic boron nitride sintered body.
  • the cubic boron nitride sintered body of the present invention has 10 to 90% by volume of cubic boron nitride and cubic boron nitride with respect to the entire cubic boron nitride sintered body.
  • a cubic boron nitride sintered body comprising 10 to 90% by volume of a binder phase and unavoidable impurities with respect to the entire sintered body, and the total of which is 100% by volume is preferable.
  • the binder phase of the present invention contains at least one element selected from the group consisting of Zr, Hf, V, Nb, Ta, Cr, Mo, and W and a composite solid solution compound of Ti.
  • a composite solid solution compound of the present invention for example, at least one element selected from the group consisting of Zr, Hf, V, Nb, Ta, Cr, Mo and W, a composite solid solution carbide of Ti, a composite solid solution nitride, Composite solid solution carbonitride, composite solid solution carbonitride, composite solid solution carbonitride, composite solid solution carbonitride, composite solid solution carbonitride, composite solid solution carbonate, composite solid solution nitride, composite solid solution carbonitride, composite solid solution carbonitride, composite solid solution carbonitride, composite Mention may be made of a compound with at least one selected from the group consisting of solid solution boron nitride, composite solid solution carbonitride and their mutual solid solutions.
  • X represents the atomic ratio of M to the sum of Ti and M
  • y represents the atomic ratio of N to the sum of C and N
  • x and y are 0.02 ⁇ x ⁇ 0. 5 and 0 ⁇ y ⁇ 1) is more preferable since it is excellent in wear resistance.
  • the binder phase of the present invention may be composed only of a composite solid solution compound, but in addition to the composite solid solution compound, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Fe, Co and Ni At least one element selected from the group consisting of carbide, nitride, boride, silicide, carbonitride, carbonitride, carbonitride, boronitride, nitrogenitride, boron silicide, carbonitride And at least one selected from the group consisting of fluoride, carbonitride, boron nitride, borocarbonitride and their mutual solid solutions, Fe, Co, Ni, Cr, Mo, W and alloys thereof. It is also preferable to contain at least one selected from the group consisting of: Examples of the binder phase other than the composite solid solution compound include aluminum compounds such as aluminum oxide, aluminum nitride, and aluminum boride, and titanium boride.
  • a composite solid solution compound powder can be added to obtain the binder phase of the present invention.
  • Ti compounds such as Ti (C, N), TiC, and TiN have been used as the binder phase.
  • the composite solid solution compound of the present invention is at least one kind of M selected from the group consisting of Zr, Hf, V, Nb, Ta, Cr, Mo, and W in a Ti compound such as Ti (C, N), TiC, and TiN. Is a solid solution, and is harder than the Ti compound. It can be confirmed by X-ray diffraction measurement that the cubic boron nitride sintered body contains the composite solid solution compound.
  • the solid solution amount of M in the composite solid solution compound in the cubic boron nitride sintered body is estimated by the atomic ratio of Ti and M in the binder phase obtained by energy dispersive X-ray spectroscopy (EDS). I can do it.
  • EDS energy dispersive X-ray spectroscopy
  • the atomic ratio of M to the total of Ti and M contained in the whole binder phase is less than 0.02, the effect of hardening the composite solid solution compound due to solid solution of M cannot be sufficiently obtained.
  • the half-value width of the (200) plane diffraction line of the composite solid solution compound contained in the cubic boron nitride sintered body of the present invention is 0.60 ° or more, the average particle size of the composite solid solution compound becomes fine, and the cubic crystal The mechanical strength of the boron nitride sintered body is improved.
  • the half-value width of the (200) plane diffraction line of the composite solid solution compound is larger than 0.90 °, the average particle size of the composite solid solution compound becomes too fine and the thermal conductivity is lowered. Therefore, the half width of the (200) plane diffraction line of the composite solid solution compound is set to 0.60 ° or more and 0.90 ° or less.
  • the Bragg angle 2 ⁇ and half width of the (200) plane diffraction line of the composite solid solution compound can be measured using a commercially available X-ray diffractometer.
  • X-ray diffractometer For example, an X-ray diffraction measurement of a 2 ⁇ / ⁇ concentrated optical system using Cu—K ⁇ rays using a Rigaku X-ray diffractometer RINT TTRIII, output: 50 kV, 250 mA, incident side solar slit: 5 ° Divergence longitudinal slit: 1/2 °, divergence longitudinal restriction slit: 10 mm, scattering slit 2/3 °, light receiving side solar slit: 5 °, light receiving slit: 0.15 mm, BENT monochromator, light receiving monochrome slit: 0.8 mm
  • Sampling width 0.02 °, scan speed: 0.1 ° / min, 2 ⁇ measurement range: 40-46 °, Bragg angle 2 ⁇ and half value for (200) plane d
  • the (200) plane diffraction line of the composite solid solution compound is a PDF card No. of International Centre for Diffraction Data Powder Diffraction File PDF-2 Release 2004 (hereinafter referred to as PDF card). No. 32-1383 TiC (200) plane diffraction line and PDF card no. It appears between the (200) plane diffraction lines of TiN described in 38-1420.
  • analysis software attached to the X-ray diffraction apparatus may be used. The analysis software performs background processing and K ⁇ 2 peak removal using cubic approximation, performs profile fitting using the Pearson-VII function, obtains the peak position by the peak top method, Bragg angle 2 ⁇ and half width Is derived.
  • the peak height of the (200) plane diffraction line of the composite solid solution compound obtained when the measurement range of the Bragg angle 2 ⁇ is 30 ° to 90 ° by X-ray diffraction measurement of 2 ⁇ / ⁇ method using Cu—K ⁇ rays.
  • the highest peak height ratio of I 2 in the diffraction line of the compound or a metal contained in the binder phase other than the complex compound (I 2 / I 1) is 1.0 or less with respect to I 1 is, the binder phase
  • the ratio of the composite solid solution compound to occupy increases, and the wear resistance is improved.
  • the peak height ratio (I 2 / I 1 ) is more preferably 0.7 or less, and the peak height ratio (I 2 / I 1 ) is more preferably 0.4 or less.
  • analysis software attached to the X-ray diffractometer may be used. In the analysis software, background processing and K ⁇ 2 peak removal are performed using cubic approximation, profile fitting is performed using the Pearson-VII function, peak positions are obtained by the peak top method, peak height I 1 and peak Height I 2 is derived.
  • the cubic boron nitride sintered body of the present invention includes a binder phase composed of at least one aluminum compound among aluminum oxide, aluminum nitride, and aluminum boride, a composite solid solution compound, and titanium boride
  • the crystal boron nitride sintered body has a good balance between wear resistance and toughness, and when used as a tool, the effect of further extending the tool life is obtained, which is preferable. This is due to the following reason.
  • at least one aluminum compound among aluminum oxide, aluminum nitride, and aluminum boride is included, toughness is improved.
  • a composite solid solution compound is included, wear resistance is improved.
  • titanium boride is included, toughness is improved.
  • Examples of the impurities inevitably contained in the cubic boron nitride sintered body of the present invention include lithium contained in the raw material powder. Since the total amount of inevitable impurities can be usually suppressed to 1% by mass or less with respect to the entire cubic boron nitride sintered body, the characteristic value of the present invention is not affected.
  • a binder phase, and unavoidable impurities in addition to the cubic boron nitride sintered body of the present invention, other than inevitable impurities can be said. You may contain a small amount of ingredients.
  • the coating layer of the present invention is not particularly limited as long as it is used as a coating layer of a coated tool, but is composed of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Y, Al, and Si.
  • a metal comprising at least one metal element selected from the group, and a compound comprising at least one metal element selected from the group consisting of at least one non-metal element selected from the group consisting of carbon, nitrogen, oxygen and boron. It is more preferable that the layer is at least one single layer or laminated layer selected from the group because wear resistance is improved. Specific examples include TiN, TiC, TiCN, TiAlN, TiSiN, and CrAlN.
  • the coating layer is preferably either a single layer or a laminate of two or more layers, and preferably has an alternately laminated structure in which two or more layers having an average layer thickness of 5 to 500 nm having different compositions are alternately laminated.
  • the total layer thickness of the entire coating layer is an average layer thickness, and if it is less than 0.5 ⁇ m, the wear resistance is lowered, and if it exceeds 20 ⁇ m, the chipping resistance is lowered. Therefore, it is preferably 0.5 to 20 ⁇ m. .
  • the cubic boron nitride sintered body of the present invention has an average in which the atomic ratio of M to the total of titanium and M is 0.02 to 0.5, and the atomic ratio of carbon to the total of carbon and nitrogen is 0 to 1.
  • a composite solid solution compound powder having a particle size of 0.01 to 0.1 ⁇ m, an aluminum powder, a cubic boron nitride powder, and paraffin are mixed, and the resultant mixture is molded, and the pressure is 1.33 ⁇ 10 ⁇ 1 Pa.
  • vacuum heat treatment is performed at a temperature of 400 to 500 ° C. in the following vacuum to remove organic substances such as paraffin, heating is further performed at 700 to 1000 ° C. under the same vacuum pressure to perform preliminary sintering.
  • cubic boron nitride sintered body and the coated cubic boron nitride sintered body of the present invention are excellent in wear resistance, fracture resistance, and toughness, they are preferably applied to cutting tools and wear resistant tools. More preferably, it is applied to a tool.
  • the cubic boron nitride sintered body and the coated cubic boron nitride sintered body of the present invention are excellent in wear resistance, fracture resistance and toughness. Therefore, when the cubic boron nitride sintered body and the coated cubic boron nitride sintered body of the present invention are used as a cutting tool or a wear-resistant tool, an effect that the tool life can be extended is obtained.
  • Example 1 A cubic boron nitride (cBN) powder having an average particle size of 2 ⁇ m, a composite solid solution compound powder having the composition and average particle size shown in Table 1 or a Ti (C 0.5 N 0.5 ) powder, and an Al powder having an average particle size of 2 ⁇ m. And blended into the composition shown in Table 1.
  • the average particle size of the raw material powder was measured by the Fisher method (Fisher Sub-Sieve Sizer (FSSS)) described in the American Society for Testing and Materials (ASTM) Standard B330.
  • the blended raw material powder was placed in a ball mill cylinder together with a cemented carbide ball, a hexane solvent, and paraffin, and ball mill mixed.
  • the mixed powder obtained by mixing and pulverizing with a ball mill was compacted.
  • the mixed powder molded body is put into a vacuum heating furnace, the inside of the furnace is evacuated to a pressure of 1.33 ⁇ 10 ⁇ 3 Pa or less, deparaffinized at a temperature of 450 ° C., heated to a pressure
  • Temporary sintering was performed at a temperature of 850 ° C. in a vacuum of 1.33 ⁇ 10 ⁇ 3 Pa or less.
  • the obtained temporary sintered body is sealed in a metal capsule, and the metal capsule is put into an ultra-high pressure and high temperature generator, and sintered under the conditions of pressure 5.5 GPa, temperature 1500 ° C., and holding time 30 minutes.
  • a comparative cubic boron nitride sintered body was obtained.
  • the cubic boron nitride sintered body thus obtained was subjected to scanning electron microscope (SEM) observation, EDS measurement, wavelength dispersive X-ray spectroscopy (WDS) measurement, X-ray diffraction measurement, and cubic boron nitride sintered. Body composition was examined. Further, the cross-sectional structure of the cubic boron nitride sintered body was observed with an SEM, and the volume% of cubic boron nitride (cBN) and the volume% of the binder phase were measured. The composition of the composite solid solution compound of the binder phase was confirmed as follows.
  • Ti and M are contained in the binder phases of Inventions 1 to 12 and Comparative Product 1 in the ratios shown in Table 4.
  • the ratio of Ti and M contained in the binder phase was the same as the ratio of Ti and M of the composite solid solution compound powder of the raw material powder. Therefore, when X-ray diffraction measurement was performed on the composite solid solution compound powder of the raw material powder, NaCl between the diffraction line of TiC diffraction line and the TiN diffraction line was found. The Bragg angle 2 ⁇ of the diffraction line of the compound having the structure coincided.
  • the composition of the compound having the NaCl structure was made the same as that of the composite solid solution compound powder of the raw material powder.
  • a diffraction line having a NaCl structure was observed between the TiC diffraction line and the TiN diffraction line. From the results of EDS measurement and WDS measurement, as shown in Table 4, the binder phase of Comparative product 2 contained Ti.
  • the inventive cubic boron nitride sintered body has higher hardness Hv and fracture toughness value K 1C than the comparative cubic boron nitride sintered body, and as a result, wear resistance and fracture resistance during cutting.
  • the tool life is longer than that of the comparative product in continuous cutting and weak interrupted cutting.
  • Example 2 A cubic boron nitride (cBN) powder having an average particle diameter of 2 ⁇ m, a composite solid solution compound powder having the composition and average particle diameter shown in Table 7 or a Ti (C 0.5 N 0.5 ) powder, and an Al powder having an average particle diameter of 2 ⁇ m. And blended into the blending composition shown in Table 7.
  • the average particle size of the raw material powder was measured by the Fisher method (Fisher Sub-Sieve Sizer (FSSS)) described in the American Society for Testing and Materials (ASTM) Standard B330.
  • the blended raw material powder was placed in a ball mill cylinder together with a cemented carbide ball, a hexane solvent, and paraffin, and ball mill mixed.
  • the mixed powder obtained by mixing and pulverizing with a ball mill was compacted.
  • the mixed powder molded body is put into a vacuum heating furnace, the inside of the furnace is evacuated to a pressure of 1.33 ⁇ 10 ⁇ 3 Pa or less, deparaffinized at a temperature of 450 ° C., heated to a pressure
  • Temporary sintering was performed at a temperature of 850 ° C. in a vacuum of 1.33 ⁇ 10 ⁇ 3 Pa or less.
  • the obtained temporary sintered body is sealed in a metal capsule, and the metal capsule is put into an ultra-high pressure and high temperature generator, and sintered under the conditions of pressure 5.5 GPa, temperature 1500 ° C., and holding time 30 minutes.
  • a comparative cubic boron nitride sintered body was obtained.
  • the cubic boron nitride sintered body thus obtained was subjected to SEM observation, EDS measurement, WDS measurement, and X-ray diffraction measurement to examine the composition of the sintered body. Further, the cross-sectional structure of the cubic boron nitride sintered body was observed with an SEM, and the volume% of cubic boron nitride (cBN) and the volume% of the binder phase were measured. The composition of the composite solid solution compound of the binder phase was confirmed as follows. When X-ray diffraction measurement was performed on Invention Products 13 to 24 and Comparative Product 3, between the diffraction line of TiC (PDF card No. 32-1383) and the diffraction line of TiN (PDF card No.
  • the binder phase of the comparative product 4 contained Ti.
  • Ti (C 0.5 N 0.5) X-ray diffraction measurement of the powder of the raw material powder, the raw material powder Ti (C 0.5 N 0.5) and the Bragg angle 2 ⁇ of the diffraction lines of the powder, NaCl Since the Bragg angle 2 ⁇ of the diffraction line of the compound having the structure coincided with that of the compound having the structure, the composition of the compound having the NaCl structure was Ti (C 0.5 N 0.5 ).
  • the inventive cubic boron nitride sintered body has higher hardness Hv and fracture toughness value K 1C than the comparative cubic boron nitride sintered body, and as a result, wear resistance and fracture resistance during cutting.
  • the tool life is longer than conventional products in continuous cutting and weak interrupted cutting.
  • Example 3 A cubic boron nitride (cBN) powder having an average particle diameter of 2 ⁇ m, a composite solid solution compound powder or Ti (C 0.5 N 0.5 ) powder having the composition and average particle diameter shown in Table 13, and an Al powder having an average particle diameter of 2 ⁇ m. And blended into the blending composition shown in Table 13.
  • the average particle size of the raw material powder was measured by the Fisher method (Fisher Sub-Sieve Sizer (FSSS)) described in the American Society for Testing and Materials (ASTM) Standard B330.
  • the blended raw material powder was placed in a ball mill cylinder together with a cemented carbide ball, a hexane solvent, and paraffin, and ball mill mixed.
  • the mixed powder obtained by mixing and pulverizing with a ball mill was compacted.
  • the mixed powder molded body is put into a vacuum heating furnace, the inside of the furnace is evacuated to a pressure of 1.33 ⁇ 10 ⁇ 3 Pa or less, deparaffinized at a temperature of 450 ° C., heated to a pressure
  • Temporary sintering was performed at a temperature of 850 ° C. in a vacuum of 1.33 ⁇ 10 ⁇ 3 Pa or less.
  • the obtained temporary sintered body is sealed in a metal capsule, and the metal capsule is put into an ultra-high pressure and high temperature generator, and sintered under the conditions of pressure 5.5 GPa, temperature 1500 ° C., and holding time 30 minutes.
  • a comparative cubic boron nitride sintered body was obtained.
  • the cubic boron nitride sintered body thus obtained was subjected to SEM observation, EDS measurement, WDS measurement, and X-ray diffraction measurement to examine the composition of the cubic boron nitride sintered body. Further, the cross-sectional structure of the cubic boron nitride sintered body was observed with an SEM, and the volume% of cubic boron nitride (cBN) and the volume% of the binder phase were measured. The composition of the composite solid solution compound of the binder phase was confirmed as follows. When X-ray diffraction measurement was performed on the inventive products 25 to 36 and the comparative product 5, between the diffraction line of TiC (PDF card No.
  • the ratio of Ti and M contained in the binder phase was the same as the ratio of Ti and M of the composite solid solution compound powder of the raw material powder. Therefore, when X-ray diffraction measurement was performed on the composite solid solution compound powder of the raw material powder, a NaCl between the Bragg angle 2 ⁇ of the diffraction line of the composite solid solution compound powder of the raw material powder and the diffraction lines of TiC and TiN was obtained. The Bragg angle 2 ⁇ of the diffraction line of the compound having the structure coincided. From these results, the composition of the compound having the NaCl structure was set to the same composition as the composite solid solution compound powder of the raw material powder.
  • the binder phase of the comparative product 6 contained Ti.
  • Example 2 About the obtained cubic boron nitride sintered compact, in order to measure the half-value width and peak height of a diffraction line, the same measurement conditions as Example 1 were used using Rigaku Co., Ltd. X-ray diffraction apparatus RINT TTRIII. The X-ray diffraction measurement was performed. From the obtained X-ray diffraction pattern, the diffraction line of TiC (PDF card No. 32-1383) and TiN (PDF) were used in the same manner as in Example 1 using the XRD analysis software JADE6 manufactured by MDI.
  • the inventive cubic boron nitride sintered body has higher hardness Hv and fracture toughness value K 1C than the comparative cubic boron nitride sintered body, and as a result, wear resistance and fracture resistance during cutting.
  • the tool life is longer than conventional products in continuous cutting and weak interrupted cutting.
  • Example 4 The surface of Invention 1 of Example 1 was coated using a PVD apparatus.
  • Invented product 37 in which the surface of a cubic boron nitride sintered body is coated with a TiN layer having an average layer thickness of 3 ⁇ m.
  • the inventive products 37 and 38 were subjected to the same cutting tests (1) and (2) as in Example 1. The results are shown in Table 19.
  • inventive products 37 and 38 coated with the coating layer were able to further extend the tool life compared to the inventive product 1 not coated with the coating layer.
  • the cubic boron nitride sintered body and the coated cubic boron nitride sintered body of the present invention are excellent in wear resistance, fracture resistance, and toughness, and particularly when used as a cutting tool or wear resistant tool. Since it can be extended, industrial applicability is high.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Ceramic Engineering (AREA)
  • Organic Chemistry (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Structural Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Ceramic Products (AREA)
  • Cutting Tools, Boring Holders, And Turrets (AREA)

Abstract

L'objet de la présente invention est de proposer un objet fritté contenant du nitrure de bore cubique et présentant une remarquable résistance à l'usure et à l'ébréchure. Ledit objet fritté à base de nitrure de bore cubique comprend du nitrure de bore cubique, une phase de liant et les inévitables impuretés, ladite phase de liant comprenant au moins un élément choisi dans le groupe constitué des éléments suivants : Zr, Hf, V, Nb, Ta, Cr, Mo et W, et un composé de Ti composite solide-en solution, ledit composé de Ti composite solide-en solution présentant une structure de type NaCl et donnant, lors d'un examen par diffraction des rayons X conduit par le procédé 2θ/θ utilisant une raie CuKα, une raie de diffraction attachée au plan (200) du composé composite solide-en solution, ladite raie de diffraction présentant une demi-largeur de bande variant de 0,60° à 0,90°.
PCT/JP2014/061685 2013-04-26 2014-04-25 Objet fritté à base de nitrure de bore cubique et objet fritté revêtu à base de nitrure de bore cubique WO2014175419A1 (fr)

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CN107001155A (zh) * 2014-11-27 2017-08-01 三菱综合材料株式会社 立方晶氮化硼基烧结体及立方晶氮化硼基烧结体制切削工具
CN107434415A (zh) * 2017-06-12 2017-12-05 金华中烨超硬材料有限公司 一种高热稳定性和良好导热性的聚晶立方氮化硼复合片及其生产方法
CN111057925A (zh) * 2019-12-31 2020-04-24 富耐克超硬材料股份有限公司 聚晶金刚石立方氮化硼复合片及其制备方法
CN114144392A (zh) * 2019-07-18 2022-03-04 住友电气工业株式会社 立方晶氮化硼烧结体
CN114144393A (zh) * 2019-07-18 2022-03-04 住友电气工业株式会社 立方晶氮化硼烧结体
CN114787104A (zh) * 2019-12-16 2022-07-22 住友电气工业株式会社 立方晶氮化硼烧结体
CN114845974A (zh) * 2019-12-16 2022-08-02 住友电工硬质合金株式会社 立方晶氮化硼烧结体及其制造方法
CN116568434A (zh) * 2020-12-25 2023-08-08 京瓷株式会社 刀片和切削刀具

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JP6933017B2 (ja) * 2017-06-29 2021-09-08 三菱マテリアル株式会社 立方晶窒化ほう素基焼結体および切削工具
JPWO2020179809A1 (fr) * 2019-03-05 2020-09-10
JP6908798B2 (ja) * 2019-07-18 2021-07-28 住友電気工業株式会社 立方晶窒化硼素焼結体
CN114144391B (zh) * 2019-07-18 2023-04-18 住友电气工业株式会社 立方晶氮化硼烧结体
CN114096502B (zh) 2019-07-18 2023-03-21 住友电气工业株式会社 立方晶氮化硼烧结体及其制造方法
JP6912685B2 (ja) * 2019-07-18 2021-08-04 住友電気工業株式会社 立方晶窒化硼素焼結体
GB202001369D0 (en) * 2020-01-31 2020-03-18 Element Six Ltd Polycrystalline cubic boron nitride material

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CN107001155A (zh) * 2014-11-27 2017-08-01 三菱综合材料株式会社 立方晶氮化硼基烧结体及立方晶氮化硼基烧结体制切削工具
CN107001155B (zh) * 2014-11-27 2020-09-18 三菱综合材料株式会社 立方晶氮化硼基烧结体及立方晶氮化硼基烧结体制切削工具
CN107434415A (zh) * 2017-06-12 2017-12-05 金华中烨超硬材料有限公司 一种高热稳定性和良好导热性的聚晶立方氮化硼复合片及其生产方法
CN114144392A (zh) * 2019-07-18 2022-03-04 住友电气工业株式会社 立方晶氮化硼烧结体
CN114144393A (zh) * 2019-07-18 2022-03-04 住友电气工业株式会社 立方晶氮化硼烧结体
CN114144393B (zh) * 2019-07-18 2023-06-23 住友电气工业株式会社 立方晶氮化硼烧结体
CN114787104A (zh) * 2019-12-16 2022-07-22 住友电气工业株式会社 立方晶氮化硼烧结体
CN114845974A (zh) * 2019-12-16 2022-08-02 住友电工硬质合金株式会社 立方晶氮化硼烧结体及其制造方法
CN114845974B (zh) * 2019-12-16 2023-10-27 住友电工硬质合金株式会社 立方晶氮化硼烧结体及其制造方法
CN111057925A (zh) * 2019-12-31 2020-04-24 富耐克超硬材料股份有限公司 聚晶金刚石立方氮化硼复合片及其制备方法
CN111057925B (zh) * 2019-12-31 2021-08-20 富耐克超硬材料股份有限公司 聚晶金刚石立方氮化硼复合片及其制备方法
CN116568434A (zh) * 2020-12-25 2023-08-08 京瓷株式会社 刀片和切削刀具

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