WO2013069657A1 - 立方晶窒化硼素焼結体 - Google Patents

立方晶窒化硼素焼結体 Download PDF

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Publication number
WO2013069657A1
WO2013069657A1 PCT/JP2012/078774 JP2012078774W WO2013069657A1 WO 2013069657 A1 WO2013069657 A1 WO 2013069657A1 JP 2012078774 W JP2012078774 W JP 2012078774W WO 2013069657 A1 WO2013069657 A1 WO 2013069657A1
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WIPO (PCT)
Prior art keywords
boron nitride
cubic boron
sintered body
nitride sintered
binder phase
Prior art date
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PCT/JP2012/078774
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English (en)
French (fr)
Inventor
雄一郎 福島
Original Assignee
株式会社タンガロイ
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Filing date
Publication date
Application filed by 株式会社タンガロイ filed Critical 株式会社タンガロイ
Priority to JP2013542993A priority Critical patent/JP5664795B2/ja
Priority to EP12847199.2A priority patent/EP2778146B1/en
Priority to US14/356,812 priority patent/US9327352B2/en
Publication of WO2013069657A1 publication Critical patent/WO2013069657A1/ja

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    • 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
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    • C22C2026/006—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes with additional metal compounds being carbides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C26/00—Alloys containing diamond or cubic or wurtzitic boron nitride, fullerenes or carbon nanotubes
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T407/00—Cutters, for shaping
    • Y10T407/27—Cutters, for shaping comprising tool of specific chemical composition
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/26—Web or sheet containing structurally defined element or component, the element or component having a specified physical dimension
    • Y10T428/263—Coating layer not in excess of 5 mils thick or equivalent
    • Y10T428/264—Up to 3 mils
    • Y10T428/265—1 mil or less
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T428/00—Stock material or miscellaneous articles
    • Y10T428/31504—Composite [nonstructural laminate]
    • Y10T428/31678—Of metal

Definitions

  • the present invention relates to a cubic boron nitride sintered body having a high cubic boron nitride content.
  • Cubic boron nitride has excellent strength as a tool material that has the second highest hardness and excellent thermal conductivity after diamond and has a lower affinity with iron than diamond.
  • many studies have been made on a cubic boron nitride sintered body having a high cubic boron nitride content.
  • cubic boron nitride sintered bodies having a high cubic boron nitride content include cubic boron nitride: 88 to 97% by volume, carbides, nitrides, borides of W, Co, and Al, and solid solutions thereof.
  • a cubic boron nitride sintered body composed of a binder phase consisting of at least one selected from the above and inevitable impurities: the balance, wherein the binder phase contains B 6 Co 21 W 2 and B 6
  • the binder phase contains B 6 Co 21 W 2 and B 6
  • the intensity ratio indicating the ratio of Iw to Ib is Iw / Ib.
  • a cubic boron nitride sintered body having a 0.10 to 0.40 is known (see, for example, Patent Document 1).
  • cubic boron nitride molded body including a polycrystalline lump of cubic boron nitride particles present in an amount of at least 70 volume percent and a binder phase that is a metal in nature (see, for example, Patent Document 2). .).
  • the invention of the above-mentioned Patent Document 1 has a problem that it has become unable to sufficiently meet the demands in recent cutting work in terms of fracture resistance and toughness.
  • the binder phase which is a metal is easily worn and wear resistance is low.
  • the present invention has been made to solve the above problems, and an object of the present invention is to provide a cubic boron nitride sintered body excellent in wear resistance and fracture resistance.
  • the inventor has conducted research on a cubic boron nitride sintered body, and as a result of improving the binder phase, the bonding of cubic boron nitride particles becomes stronger, and the toughness of the cubic boron nitride sintered body is improved. I got the knowledge. In addition, it was also found that the wear of the cubic boron nitride sintered body can be suppressed by changing the binder phase of the cubic boron nitride sintered body from a metal to a compound, thereby reducing the wear of the binder phase.
  • the gist of the present invention is as follows.
  • Cubic boron nitride is composed of 85 to 95% by volume, and a binder phase and inevitable impurities: 5 to 15% by volume, and the binder phase includes Al, V, Cr, Mn, Co, Ni, Nb and Consisting of three or more compounds selected from the group consisting of carbides, nitrides, carbonitrides, oxides and their mutual solid solutions selected from the group consisting of Mo and included in the cubic boron nitride sintered body
  • the amount of aluminum element to be added is 0.5 to 5% by mass with respect to the total mass of the cubic boron nitride sintered body, provided that the binder phase does not include simple metals and alloys. Boron sintered body.
  • the binder phase is a carbide, nitride, or carbonitride of an element selected from the group consisting of at least one compound of AlN and Al 2 O 3 and V, Cr, Mn, Co, Ni, Nb, and Mo. And a cubic boron nitride sintered body according to (1), which comprises two or more compounds selected from the group consisting of a solid solution and a mutual solid solution thereof.
  • the binder phase is selected from the group consisting of at least one compound of AlN and Al 2 O 3 and Co 5.47 N, Cr 2 N, CrN, Cr 3 C 2 , Mo 2 C and VC.
  • the amount of tungsten element contained in the cubic boron nitride sintered body is 5% by mass or less based on the total mass of the cubic boron nitride sintered body, according to any one of (1) to (5) Cubic boron nitride sintered body.
  • the simple metal and alloy not included in the binder phase are metals in which the single metal is composed of one kind of metal element, and the alloy is a metal composed of two or more kinds of metal elements
  • (1) The coated cubic boron nitride sintered body according to any one of (6) to (6).
  • At least one metal selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, and Si, and at least one oxide or carbide of these metals The coated cubic boron nitride sintered body according to (9), comprising at least one selected from the group consisting of nitrides, borides, and mutual solid solutions thereof.
  • 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.
  • the cubic boron nitride sintered body of the present invention has a cubic boron nitride: 85 to 95% by volume with respect to the total mass of the cubic boron nitride sintered body, a binder phase and inevitable impurities: cubic boron nitride sintered.
  • the cubic boron nitride sintered body is composed of 5 to 15% by volume with respect to the total mass of the body, and the total of these is 100% by volume.
  • the amount of cubic boron nitride exceeds 95% by volume and the binder phase and unavoidable impurities are less than 5% by volume, the cubic boron nitride particles easily fall off.
  • cubic boron nitride when the cubic boron nitride is less than 85% by volume and the binder phase and inevitable impurities are more than 15% by volume, the wear resistance of the cubic boron nitride sintered body is lowered. Therefore, cubic boron nitride was set to 85 to 95% by volume, and the binder phase and unavoidable impurities were set to 5 to 15% by volume. Among them, cubic boron nitride: 89 to 95% by volume, and the balance is preferably a binder phase and inevitable impurities.
  • the cubic boron nitride and the content (volume%) of the binder phase and inevitable impurities were photographed at 1000 to 5000 times by photographing the cross-sectional structure of the cubic boron nitride sintered body with an SEM (scanning electron microscope).
  • the cross-sectional structure photograph can be image-analyzed and obtained from each surface area ratio.
  • the binder phase of the present invention is selected from the group consisting of carbides, nitrides, carbonitrides, oxides and their mutual solid solutions of elements selected from Al, V, Cr, Mn, Co, Ni, Nb and Mo. It consists of three or more compounds. Preferably, at least one of AlN (PDF card No. 25-1133) and Al 2 O 3 (PDF card No. 10-0173), V, Cr, Mn, Co, Ni, Nb, Mo carbide, nitriding And two or more selected from the group consisting of solids, carbonitrides and their mutual solid solutions.
  • PDF card no. Is a number identifying a substance described in Powder Diffraction File PDF-2 Release 2004 of International Center for Diffraction Data. Since the binder phase of the present invention is composed of these compounds and does not contain simple metals or alloys, the wear of the binder phase can be suppressed.
  • the simple metal means a metal composed of one kind of metal element
  • the alloy means a metal composed of two or more kinds of metal elements.
  • an intermetallic compound in which two or more metal elements are bonded at a certain ratio is a kind of alloy, and the binder phase of the present invention does not include an intermetallic compound. That is, since the entire cubic boron nitride sintered body does not contain a single metal or an alloy, the effect of improving the wear resistance of the cubic boron nitride sintered body can be obtained.
  • the binder phase of the present invention is selected from the group consisting of at least one of AlN and Al 2 O 3 and Co 5.47 N, CrN, Cr 2 N, Cr 3 C 2 , Mo 2 C and VC 2 More preferably, it comprises more than seeds, and among them, it is more preferred that the binder phase contains Co 5.47 N and Cr 2 N, and among these, the binder phase comprises Al 2 O 3 , AlN, Co 5.47 N and Cr 2 N. More preferably.
  • the cubic boron nitride sintered body of the present invention contains 0.5 to 5% by mass of aluminum element with respect to the total mass of the cubic boron nitride sintered body.
  • Aluminum element combines with oxygen adsorbed on the raw material powder, and has the effect of strengthening the bond between cubic boron nitride particles and the binder phase.
  • the amount of aluminum element contained in the cubic boron nitride sintered body is less than 0.5% by mass, the action of combining with oxygen is insufficient and the cubic boron nitride particles are likely to fall off.
  • the amount of aluminum element contained in the cubic boron nitride sintered body of the present invention is set to 0.5 to 5% by mass with respect to the total mass of the cubic boron nitride sintered body.
  • the aluminum element amount is preferably 0.5 to 4% by mass with respect to the total mass of the cubic boron nitride sintered body.
  • the amount of aluminum element in the cubic boron nitride sintered body of the present invention can be measured using an EDS (energy dispersive X-ray analyzer) or the like.
  • the average particle size of the cubic boron nitride of the present invention is not particularly limited. However, when the average particle size of the cubic boron nitride is less than 0.5 ⁇ m, the surface adsorbed oxygen amount of the cubic boron nitride increases and the average particle size is increased. The sintering reaction tends to be hindered and the sinterability tends to decrease. When the average particle size exceeds 5 ⁇ m, the binder phase tends to aggregate and the thickness of the brittle binder phase is larger than that of cubic boron nitride. Therefore, the average particle size of the cubic boron nitride of the present invention is preferably 0.5 to 5 ⁇ m. Among these, the average particle diameter of cubic boron nitride is more preferably 1 to 3 ⁇ m.
  • Examples of impurities inevitably contained in the cubic boron nitride sintered body of the present invention include lithium element mixed from the raw material powder and tungsten element mixed in the mixing step of the raw material powder.
  • the total amount of inevitable impurities is generally 5% by mass or less with respect to the total mass of the cubic boron nitride sintered body, and more preferably 3% by mass or less.
  • tungsten element is contained in the cubic boron nitride sintered body as a compound such as WC and WB. There is a tendency for the cutting performance of the boron nitride sintered body to decrease.
  • the amount of tungsten element contained in the cubic boron nitride sintered body of the present invention is preferably 5% by mass or less with respect to the total mass of the cubic boron nitride sintered body because cutting performance is improved. More preferably, the amount of tungsten element is 3% by mass or less. Most of the tungsten element contained as an inevitable impurity in the cubic boron nitride sintered body of the present invention is derived from a cemented carbide ball used for ball mill mixing.
  • the amount of tungsten element contained in the cubic boron nitride sintered body of the present invention is adjusted by adjusting the composition of the cemented carbide ball, the amount of the cemented carbide ball used, the size of the cylinder, and the ball mill mixing time. Can be adjusted.
  • the amount of tungsten element contained in the cubic boron nitride sintered body of the present invention can be measured using an EDS (energy dispersive X-ray analyzer) or the like.
  • At least one metal selected from Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al and Si, at least one oxide of these metals, carbide Mention may be made of at least one selected from the group consisting of nitrides, borides and their mutual solid solutions. Specific examples include TiN, TiC, TiCN, TiAlN, TiSiN, and CrAlN.
  • the coating is preferably either a single layer or a laminate of two or more layers, and is also preferably an alternately laminated film in which thin films having different film thicknesses of 5 to 200 nm are alternately laminated. When the average film thickness is less than 0.5 ⁇ m, the effect of extending the tool life is reduced. When the average film thickness exceeds 15 ⁇ m, the fracture resistance tends to decrease. It is preferably 15 ⁇ m, more preferably 1 to 10 ⁇ m, and most preferably 1.5 to 5 ⁇ m.
  • 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, they are preferably used as cutting tools and wear resistant tools. More preferably, it is used as a tool, and more preferably, it is used as a cutting tool for sintered metal or a cutting tool for cast iron.
  • the cubic boron nitride sintered body of the present invention can be obtained, for example, by the following manufacturing method.
  • raw material powders cubic boron nitride powder having an average particle size of 0.5 to 8 ⁇ m, aluminum powder having an average particle size of 5 to 20 ⁇ m, and V, Cr, Mn, Co, Ni, having an average particle size of 0.5 to 5 ⁇ m
  • a binder phase forming powder composed of two or more selected from the group consisting of Nb, Mo metal, carbide, nitride, carbonitride, and their mutual solid solution is prepared.
  • the average particle diameter of the raw material powder is measured by the Fisher method (Fisher Sub-Sieve Sizer (FSSS)) described in American Society for Testing and Materials (ASTM) standard B330.
  • the prepared raw material powders consisted of cubic boron nitride powder: 85 to 95% by volume, aluminum powder: 0.5 to 8% by volume, and binder phase forming powder: 3 to 14.5% by volume. It mix
  • the shape of aluminum powder is not specifically limited, In this invention, it can be used even if it is any shape, such as spherical shape, scale shape, and needle shape. Paraffin is added to the blended raw material powder and mixed.
  • the obtained mixture is molded and subjected to vacuum heat treatment at a temperature of 700 to 1000 ° C. in a vacuum of 5 ⁇ 10 ⁇ 3 Pa or less to remove organic substances such as paraffin, and then put into an ultrahigh pressure and high temperature generator. It is obtained by sintering under conditions of pressure 6 to 8 GPa, temperature 1700 to 2000 ° C. and holding time 20 to 60 minutes.
  • the cubic boron nitride sintered body of the present invention is processed into a predetermined shape by a laser cutting machine or the like to produce a cutting tool or wear-resistant tool provided with the cubic boron nitride sintered body of the present invention. Can do.
  • the coated cubic boron nitride sintered body of the present invention can be obtained by forming a film on the surface of the cubic boron nitride sintered body of the present invention by a conventional CVD method or PVD method.
  • cBN Cubic boron nitride
  • Cr powder having an average particle size of 4.9 ⁇ m
  • Cr 2 N powder having an average particle size of 3.0 ⁇ m
  • Cr 3 having an average particle size of 2.7 ⁇ m C 2 powder
  • VC powder with an average particle size of 2.7 ⁇ m
  • Mo 2 C powder with an average particle size of 2.5 ⁇ m
  • TiN powder with an average particle size of 1.8 ⁇ m
  • WC powder with an average particle size of 2.2 ⁇ m
  • Co powder and a scaly aluminum (Al) powder having an average particle size of 20 ⁇ m were prepared and blended in the blending composition shown in Table 1.
  • the average particle diameter of the raw material powder was measured by the Fisher method (Fisher Sub-Sieve Sizer (FSSS)) described in 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, an n-hexane solvent and paraffin, and ball mill mixing was performed for 24 hours. After the mixed powder obtained by mixing and pulverizing with a ball mill was compacted, it was deparaffinized under conditions of a pressure of 5 ⁇ 10 ⁇ 3 Pa and a temperature of 750 ° C.
  • the compacted body that has been deparaffinized is enclosed in a metal capsule, the metal capsule is placed in an ultra-high pressure and high temperature generator, and sintered under a pressure of 7.0 GPa, a temperature of 1900 ° C., and a holding time of 30 minutes. Cubic boron nitride sintered bodies were obtained.
  • the cross-sectional structure of the cubic boron nitride sintered body thus obtained was observed using SEM (HITACHI SEM S-3000H), and the composition was analyzed using EDS (HORIBA EMAX EX-300).
  • EDS HORIBA EMAX EX-300.
  • the cBN content (% by volume) and the binder phase content (% by volume) were determined from the respective surface areas.
  • the amount of aluminum (Al) element (mass%) and the amount of tungsten (W) element (mass%) contained in the entire cubic boron nitride sintered body were quantitatively analyzed by EDS.
  • the cubic boron nitride sintered body is cut into a predetermined shape with a laser cutting machine, brazed to a cemented carbide base material, and subjected to grinding finish processing to form an ISO standard CNGA120408 cutting insert
  • the cutting tool was obtained.
  • the following cutting tests (1) and (2) were performed using these cutting inserts. The results are shown in Table 3.
  • Cutting test (1) Perimeter continuous wet cutting (turning), Work material: Carburized and quenched sintered metal (chemical component C: 0.2 to 1.0 mass%, Fe: remainder, other: 1 mass% or less (equivalent to the former JIS standard SMF4040), HRA 63 to 65), Work material shape: Cylinder ⁇ 45mm ⁇ 85mm, Cutting speed: 250 m / min, Cutting depth: 0.2 mm, Feed: 0.1 mm / rev, Insert shape: CNGA120408, Holder: DCLNR2525M12, Evaluation: Cutting time until the corner wear amount VBc reaches 0.15 mm or cutting time until a defect.
  • Cutting test (2) Peripheral intermittent wet cutting (turning), Work material: Sintered metal (Chemical component C: 0.2 to 1.0 mass%, Fe: remainder, others: 1 mass% or less (equivalent to the former JIS standard SMF4040), HRB 77 to 80), Work material shape: Gear shape ⁇ 45mm (tooth height 8mm) x 30mm, Cutting speed: 300 m / min, Cutting depth: 0.2 mm, Feed: 0.1 mm / rev, Insert shape: CNGA120408, Holder: DCLNR2525M12, Evaluation: Cutting time until the corner wear amount VBc reaches 0.15 mm or cutting time until a defect.
  • the cubic boron nitride sintered body of the present invention is superior in wear resistance and fracture resistance, and therefore has a longer tool life than the comparative cubic boron nitride sintered body.
  • Example 2 The raw material powder of Example 1 was blended in the blending composition shown in Table 4, and a cubic boron nitride sintered body was produced by the same production method as in Example 1.
  • the obtained cubic boron nitride sintered body was subjected to various measurements by the same measurement method as in Example 1. The results are shown in Table 5.
  • a cubic boron nitride sintered body was processed in the same manner as in Example 1 to obtain a cutting tool having an ISO standard CNGA120408 cutting insert shape. Using these cutting inserts, cutting tests (1) and (2) under the same test conditions as in Example 1 were performed. The results are shown in Table 6.
  • Example 3 The raw material powder of Example 1 was blended in the blending composition shown in Table 7, and a cubic boron nitride sintered body was produced by the same production method as in Example 1.
  • a cubic boron nitride sintered body was processed in the same manner as in Example 1 to obtain a cutting tool having an ISO standard CNGA120408 cutting insert shape. Using these cutting inserts, cutting tests (1) and (2) under the same test conditions as in Example 1 were performed. The results are shown in Table 9.
  • Example 4 The surface of Invention 1 of Example 1 was coated using a PVD apparatus.
  • Inventive product 17 was obtained by forming a TiN film having an average film thickness of 3 ⁇ m on the surface of Invention product 1
  • Invented product 18 was formed by forming a TiAlN film having an average film thickness of 3 ⁇ m on the surface of Invention product 1.
  • the inventive products 17 and 18 were subjected to the same cutting tests (1) and (2) as in Example 1. The results are shown in Table 10.
  • Inventive products 17 and 18 with a coating formed could have a longer tool life than Invention 1 without a coating.
  • a cubic boron nitride sintered body and a coated cubic boron nitride sintered body excellent in wear resistance, fracture resistance and toughness can be provided.
  • 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.

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Abstract

　本発明は、耐摩耗性および耐欠損性に優れた立方晶窒化硼素焼結体を提供することを目的とし、立方晶窒化硼素：８５～９５体積％と、結合相および不可避的不純物：５～１５体積％とから構成され、結合相は、Ａｌ、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから成る群より選択された元素の炭化物、窒化物、炭窒化物、酸化物およびこれらの相互固溶体から成る群より選択された３種以上の化合物とからなり、立方晶窒化硼素焼結体に含まれるアルミニウム元素量は立方晶窒化硼素焼結体の全質量に対して０．５～５質量％であり、但し、結合相中に金属単体および合金は含まれないことを特徴とする立方晶窒化硼素焼結体を提供する。

Description

立方晶窒化硼素焼結体
　本発明は、立方晶窒化硼素含有率の高い立方晶窒化硼素焼結体に関する。
　立方晶窒化硼素（ｃＢＮ）は、ダイヤモンドに次ぐ高い硬度と優れた熱伝導性を持ち、しかもダイヤモンドに比べて鉄との親和性が低いという工具材料としての優れた長所を有している。近年、立方晶窒化硼素含有率の高い立方晶窒化硼素焼結体について多くの検討がなされている。
　立方晶窒化硼素含有率が高い立方晶窒化硼素焼結体の従来技術としては、立方晶窒化硼素：８８～９７体積％と、Ｗ、Ｃｏ、Ａｌの炭化物、窒化物、硼化物およびこれらの固溶体の中から選ばれた少なくとも１種からなる結合相と不可避不純物：残部とで構成された立方晶窒化硼素焼結体であって、結合相はＢ6Ｃｏ21Ｗ2を含有するとともに、Ｂ6Ｃｏ21Ｗ2の（４２０）面のＸ線回折強度をＩｗ、立方晶窒化硼素の（１１１）面のＸ線回折強度をＩｂと表したとき、Ｉｂに対するＩｗの割合を示す強度比Ｉｗ／Ｉｂが０．１０～０．４０となる立方晶窒化硼素焼結体が知られている（例えば、特許文献１参照。）。
　また、少なくとも７０体積パーセントの量で存在する立方晶窒化硼素粒子の多結晶塊と、性質上金属であるバインダ相とを含む立方晶窒化硼素成形体が知られている（例えば、特許文献２参照。）。
特開２００４－３３１４５６号公報 特開２０１０－５１２３００号公報
　しかしながら、上記特許文献１の発明は、耐欠損性および靭性の点で、近年の切削加工における要求に対して十分に応えられなくなってきたという問題がある。また、上記特許文献２の発明では、金属である結合相が摩耗しやすく、耐摩耗性が低いという問題がある。本発明は、上記問題を解決するためになされたもので、耐摩耗性および耐欠損性に優れた立方晶窒化硼素焼結体を提供することを目的とする。
　本発明者は、立方晶窒化硼素焼結体に関する研究を行ってきたところ、結合相を改良することで立方晶窒化硼素粒子の結合が強固となり、立方晶窒化硼素焼結体の靭性が向上するとの知見を得た。また、立方晶窒化硼素焼結体の結合相を金属から化合物にすることにより、結合相の摩耗が抑えられ、立方晶窒化硼素焼結体の耐摩耗性が向上するとの知見をも得た。
　本発明の要旨は次の通りである。
（１）立方晶窒化硼素：８５～９５体積％と、結合相および不可避的不純物：５～１５体積％とから構成され、結合相は、Ａｌ、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから成る群より選択された元素の炭化物、窒化物、炭窒化物、酸化物およびこれらの相互固溶体から成る群より選択された３種以上の化合物からなり、立方晶窒化硼素焼結体に含まれるアルミニウム元素量は立方晶窒化硼素焼結体の全質量に対して０．５～５質量％であり、但し、結合相中に金属単体および合金は含まれないことを特徴とする立方晶窒化硼素焼結体。
（２）結合相は、ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種の化合物と、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから成る群より選択された元素の炭化物、窒化物、炭窒化物およびこれらの相互固溶体から成る群より選択された２種以上の化合物とからなる（１）に記載の立方晶窒化硼素焼結体。
（３）結合相は、ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種の化合物と、Ｃｏ5.47Ｎ、Ｃｒ2Ｎ、ＣｒＮ、Ｃｒ3Ｃ2、Ｍｏ2ＣおよびＶＣから成る群より選択された２種以上の化合物とからなる（１）または（２）に記載の立方晶窒化硼素焼結体。
（４）結合相は、少なくともＣｏ5.47ＮおよびＣｒ2Ｎを含有する（１）～（３）のいずれかに記載の立方晶窒化硼素焼結体。
（５）結合相は、Ａｌ2Ｏ3、ＡｌＮ、Ｃｏ5.47ＮおよびＣｒ2Ｎからなる（１）～（４）のいずれかに記載の立方晶窒化硼素焼結体。
（６）立方晶窒化硼素焼結体に含まれるタングステン元素量は、立方晶窒化硼素焼結体の全質量に対して５質量％以下である（１）～（５）のいずれかに記載の立方晶窒化硼素焼結体。
（７）結合相中に含まれない金属単体および合金は、金属単体が１種の金属元素から構成される金属であり、合金が２種以上の金属元素から構成される金属である（１）～（６）のいずれかに記載の被覆立方晶窒化硼素焼結体。
（８）切削工具または耐摩耗工具として使用される（１）～（７）のいずれかに記載の立方晶窒化硼素焼結体。
（９）（１）～（７）のいずれかに記載の立方晶窒化硼素焼結体の表面に被膜を形成した被覆立方晶窒化硼素焼結体。
（１０）被膜がＴｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗ、ＡｌおよびＳｉから成る群より選択された少なくとも１種の金属、これら金属の少なくとも１種の酸化物、炭化物、窒化物、硼化物およびこれらの相互固溶体から成る群より選択された少なくとも１種からなる（９）に記載の被覆立方晶窒化硼素焼結体。
（１１）被膜がＴｉＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＡｌＮ、ＴｉＳｉＮおよびＣｒＡｌＮから成る群より選択された少なくとも１種からなる（９）または（１０）に記載の被覆立方晶窒化硼素焼結体。
（１２）被膜の平均膜厚が、０．５～１５μｍである（９）～（１１）のいずれかに記載の被覆立方晶窒化硼素焼結体。
（１３）切削工具または耐摩耗工具として使用される（９）～（１２）のいずれかに記載の被覆立方晶窒化硼素焼結体。
　本発明の立方晶窒化硼素焼結体および被覆立方晶窒化硼素焼結体は、耐摩耗性、耐欠損性および靭性に優れる。そのため、本発明の立方晶窒化硼素焼結体および被覆立方晶窒化硼素焼結体を切削工具や耐摩耗工具として使用すると工具寿命を延長することができるという効果が得られる。
　本発明の立方晶窒化硼素焼結体は、立方晶窒化硼素：立方晶窒化硼素焼結体の全質量に対して８５～９５体積％と、結合相および不可避的不純物：立方晶窒化硼素焼結体の全質量に対して５～１５体積％とから構成され、これらの合計は１００体積％になる立方晶窒化硼素焼結体である。立方晶窒化硼素が９５体積％を超えて多くなり結合相および不可避的不純物が５体積％未満になると、立方晶窒化硼素粒子が脱落しやすくなる。逆に立方晶窒化硼素が８５体積％未満になり結合相および不可避的不純物が１５体積％を超えて多くなると、立方晶窒化硼素焼結体の耐摩耗性が低下する。このことから、立方晶窒化硼素：８５～９５体積％と、結合相および不可避的不純物：５～１５体積％とした。その中でも、立方晶窒化硼素：８９～９５体積％であり、残部が結合相および不可避的不純物であることが好ましい。立方晶窒化硼素と、結合相および不可避的不純物の含有量（体積％）は、立方晶窒化硼素焼結体の断面組織をＳＥＭ（走査型電子顕微鏡）で撮影し、１０００～５０００倍で撮影された断面組織写真を画像解析し、それぞれの表面積率から求めることができる。
　本発明の結合相は、Ａｌ、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから選択された元素の炭化物、窒化物、炭窒化物、酸化物およびこれらの相互固溶体から成る群より選択された３種以上の化合物から成る。好ましくは、ＡｌＮ（ＰＤＦカードＮｏ．２５－１１３３）およびＡｌ2Ｏ3（ＰＤＦカードＮｏ．１０－０１７３）の少なくとも１種と、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、Ｎｂ、Ｍｏの炭化物、窒化物、炭窒化物およびこれらの相互固溶体から成る群より選択された２種以上とからなるものである。ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種と、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから選択された元素の炭化物、窒化物、炭窒化物およびこれらの相互固溶体から成る群より選択された２種以上とからなる結合相とすることにより、立方晶窒化硼素粒子の結合が強固となり、立方晶窒化硼素焼結体の靭性を向上させることができた。Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏの炭化物、窒化物、炭窒化物およびこれらの相互固溶体として具体的には、ＣｒＮ（ＰＤＦカードＮｏ．１１－００６５）、Ｃｒ2Ｎ（ＰＤＦカードＮｏ．３５－０８０３）、Ｃｒ3Ｃ2（ＰＤＦカードＮｏ．３５－０８０４）、ＣｏＮ（ＰＤＦカードＮｏ．１６－０１１６）、Ｃｏ5.47Ｎ（ＰＤＦカードＮｏ．４１－０９４３）、ＶＣ（ＰＤＦカードＮｏ．３５－０７８６）、Ｍｏ2Ｃ（ＰＤＦカードＮｏ．３５－０７８７）などを挙げることができる。ここで、ＰＤＦカードＮｏ．とは、International Centre for Diffraction DataのPowder Diffraction File PDF-2 Release 2004に記載されている、物質を特定する番号である。本発明の結合相は、これらの化合物からなり、金属単体および合金を含まないので、結合相の摩耗が抑えられる。本発明において、金属単体とは１種の金属元素から構成される金属を意味し、合金とは２種以上の金属元素から構成される金属を意味する。なお、２種以上の金属元素が一定の比率で結合した金属間化合物は合金の１種であり、本発明の結合相は金属間化合物を含まない。すなわち、立方晶窒化硼素焼結体全体が金属単体および合金を含まないので、立方晶窒化硼素焼結体の耐摩耗性が向上するという効果が得られる。その中でも、本発明の結合相が、ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種と、Ｃｏ5.47Ｎ、ＣｒＮ、Ｃｒ2Ｎ、Ｃｒ3Ｃ2、Ｍｏ2ＣおよびＶＣから成る群より選択された２種以上とからなるとさらに好ましく、その中でも、結合相がＣｏ5.47ＮおよびＣｒ2Ｎを含有すると、さらに好ましく、その中でも、結合相がＡｌ2Ｏ3とＡｌＮとＣｏ5.47ＮとＣｒ2Ｎとからなると、さらに好ましい。
　本発明の立方晶窒化硼素焼結体は、アルミニウム元素を立方晶窒化硼素焼結体の全質量に対して０．５～５質量％含有する。アルミニウム元素は、原料粉末に吸着した酸素と結合して、立方晶窒化硼素粒子や結合相の結合を強化する作用がある。立方晶窒化硼素焼結体に含まれるアルミニウム元素量が０．５質量％未満になると酸素と結合する作用が不足して立方晶窒化硼素粒子が脱落しやすくなる。逆にアルミニウム元素量が５質量％を超えて多くなると、窒化アルミニウムや硼化アルミニウムが必要以上に多く生成して立方晶窒化硼素焼結体の耐摩耗性が低下する。そのため、本発明の立方晶窒化硼素焼結体に含まれるアルミニウム元素量を立方晶窒化硼素焼結体の全質量に対して０．５～５質量％とした。その中でも、アルミニウム元素量は立方晶窒化硼素焼結体の全質量に対して０．５～４質量％であることが好ましい。なお、本発明の立方晶窒化硼素焼結体のアルミニウム元素量はＥＤＳ（エネルギー分散型Ｘ線分析装置）などを用いて測定することができる。
　本発明の立方晶窒化硼素の平均粒径は特に限定されることはないが、立方晶窒化硼素の平均粒径が０．５μｍ未満となると立方晶窒化硼素の表面吸着酸素量が増加して焼結反応が阻害され、焼結性が低下する傾向がみられ、平均粒径が５μｍを超えて大きくなると結合相が凝集しやすくなり立方晶窒化硼素と比較して脆弱な結合相の厚みが大となり耐欠損性が低下する傾向がみられるので、本発明の立方晶窒化硼素の平均粒径は０．５～５μｍであると好ましい。その中でも、立方晶窒化硼素の平均粒径は１～３μｍであることがさらに好ましい。
　本発明の立方晶窒化硼素焼結体に不可避的に含有される不純物としては、原料粉末から混入されるリチウム元素や、原料粉末の混合工程で混入されるタングステン元素を挙げることができる。不可避的不純物の合計量は、一般的には立方晶窒化硼素焼結体の全質量に対して５質量％以下であり、３質量％以下に抑えることができればさらに好ましい。本発明の立方晶窒化硼素焼結体に含まれる不可避的不純物の中でもタングステン元素はＷＣやＷＢなどの化合物として立方晶窒化硼素焼結体中に含まれるが、タングステン元素が多く含まれると立方晶窒化硼素焼結体の切削性能が低下する傾向が見られる。そのため、本発明の立方晶窒化硼素焼結体に含まれるタングステン元素量が立方晶窒化硼素焼結体の全質量に対して５質量％以下であると、切削性能が向上するので好ましく、その中でもタングステン元素量が３質量％以下であると、さらに好ましい。本発明の立方晶窒化硼素焼結体の不可避的不純物として含まれるタングステン元素のほとんどが、ボールミル混合に用いる超硬合金製ボールに由来する。そのため、超硬合金製ボールの組成、超硬合金製ボールの使用量、シリンダーの大きさ、ボールミル混合時間を調整することで、本発明の立方晶窒化硼素焼結体に含まれるタングステン元素量を調整することができる。なお、本発明の立方晶窒化硼素焼結体に含まれるタングステン元素量はＥＤＳ（エネルギー分散型Ｘ線分析装置）などを用いて測定することができる。
　本発明の被膜としては、Ｔｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗ、ＡｌおよびＳｉから選択された少なくとも１種の金属、これら金属の少なくとも１種の酸化物、炭化物、窒化物、硼化物およびこれらの相互固溶体から成る群より選択された少なくとも１種からなるものを挙げることができる。具体的には、ＴｉＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＡｌＮ、ＴｉＳｉＮおよびＣｒＡｌＮなどを挙げることができる。被膜は単層または２層以上の積層のいずれでも好ましく、組成が異なる膜厚５～２００ｎｍの薄膜を交互に積層した交互積層膜でも好ましい。被膜全体の総膜厚は、平均膜厚として、０．５μｍ未満であると工具寿命を延長させる効果が小さくなり、１５μｍを超えると耐欠損性が低下する傾向を示すことから、０．５～１５μｍであると好ましく、その中でも１～１０μｍがさらに好ましく、その中でも１．５～５μｍがさらに好ましい。
　本発明の立方晶窒化硼素焼結体および被覆立方晶窒化硼素焼結体は、耐摩耗性、耐欠損性および靭性に優れるため、切削工具や耐摩耗工具として使用されると好ましく、その中でも切削工具として使用されるとさらに好ましく、その中でも焼結金属用切削工具や鋳鉄用切削工具として使用されるとさらに好ましい。
　本発明の立方晶窒化硼素焼結体は、例えば、以下の製造方法によって得ることができる。原料粉末として、平均粒径０．５～８μｍの立方晶窒化硼素粉末と、平均粒径５～２０μｍのアルミニウム粉末と、平均粒径０．５～５μｍのＶ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、Ｎｂ、Ｍｏの金属、炭化物、窒化物、炭窒化物およびこれらの相互固溶体から成る群より選択された２種以上からなる結合相形成用粉末とを用意する。なお、原料粉末の平均粒径は米国材料試験協会（ＡＳＴＭ）規格Ｂ３３０に記載のフィッシャー法（Fisher Sub-Sieve Sizer（FSSS））により測定されたものである。用意した原料粉末を、立方晶窒化硼素粉末：８５～９５体積％と、アルミニウム粉末：０．５～８体積％と、結合相形成用粉末：３～１４．５体積％とからなり、これらの合計が１００体積％となるように配合する。なお、アルミニウム粉末の形状は特に限定されず、本発明においては、球状、鱗片状、針状等いずれの形状であっても使用することができる。配合した原料粉末にパラフィンを加えて混合する。得られた混合物を成型し、圧力５×１０-3Ｐａ以下の真空中にて温度７００～１０００℃で真空熱処理を行って、パラフィンなどの有機物を除去した後、超高圧高温発生装置に入れて、圧力６～８ＧＰａ、温度１７００～２０００℃、保持時間２０～６０分の条件で焼結することで得られる。また、本発明の立方晶窒化硼素焼結体をレーザーカット加工機などにより所定の形状に加工して、本発明の立方晶窒化硼素焼結体を具えた切削工具または耐摩耗工具を製造することができる。また、本発明の立方晶窒化硼素焼結体の表面に、従来からあるＣＶＤ法またはＰＶＤ法によって被膜を形成することにより、本発明の被覆立方晶窒化硼素焼結体を得ることができる。
［実施例１］
　平均粒径２μｍの立方晶窒化硼素（以下、ｃＢＮと表す。）粉末、平均粒径４．９μｍのＣｒ粉末、平均粒径３．０μｍのＣｒ2Ｎ粉末、平均粒径２．７μｍのＣｒ3Ｃ2粉末、平均粒径２．７μｍのＶＣ粉末、平均粒径２．５μｍのＭｏ2Ｃ粉末、平均粒径１．８μｍのＴｉＮ粉末、平均粒径２．２μｍのＷＣ粉末、平均粒径０．９μｍのＣｏ粉末、平均粒径２０μｍの鱗片状アルミニウム（Ａｌ）粉末を用意して、表１に示す配合組成に配合した。なお、原料粉末の平均粒径は米国材料試験協会（ＡＳＴＭ）規格Ｂ３３０に記載のフィッシャー法（Fisher Sub-Sieve Sizer（FSSS））により測定した。配合した原料粉末を超硬合金製ボールとｎ－ヘキサン溶媒とパラフィンとともにボールミル用のシリンダーに入れてボールミル混合を２４時間行った。ボールミルで混合粉砕して得られた混合粉末を圧粉成型した後、圧力５×１０-3Ｐａ、温度７５０℃の条件で脱パラフィン処理をした。脱パラフィン処理をした圧粉成型体を金属カプセルに封入し、金属カプセルを超高圧高温発生装置に入れて、圧力７．０ＧＰａ、温度１９００℃、保持時間３０分の条件で焼結して、発明品および比較品の立方晶窒化硼素焼結体を得た。
Figure JPOXMLDOC01-appb-T000001
　こうして得られた立方晶窒化硼素焼結体の断面組織を、ＳＥＭ（ＨＩＴＡＣＨＩ製ＳＥＭ　Ｓ－３０００Ｈ）を用いて観察し、ＥＤＳ（ＨＯＲＩＢＡ製ＥＭＡＸ　ＥＸ－３００）を用いて組成を分析した。ＳＥＭにより３０００倍で撮影された断面組織写真を画像解析することで、それぞれの表面積からｃＢＮの含有量（体積％）と結合相の含有量（体積％）を求めた。また、立方晶窒化硼素焼結体全体に含まれるアルミニウム（Ａｌ）元素量（質量％）とタングステン（Ｗ）元素量（質量％）をＥＤＳで定量分析した。次に、株式会社リガク製Ｘ線回折装置ＲＩＮＴ－ＴＴＲIIIを用いて、出力：５０ｋＶ、２５０ｍＡ、Ｃｕ－Ｋα、入射側ソーラースリット：５°、発散縦スリット：１／２°、発散縦制限スリット：１０ｍｍ、散乱スリット２／３°、受光側ソーラースリット：５°、受光スリット：０．１５ｍｍ、ＢＥＮＴモノクロメータ、受光モノクロスリット：０．８ｍｍ、サンプリング幅：０．０２°、スキャンスピード：０．１°／ｍｉｎ、２θ／θ法、２θ測定範囲：３０～８０°という測定条件で、立方晶窒化硼素焼結体のＸ線回折測定を行い、立方晶窒化硼素焼結体の各相（Ａｌ2Ｏ3（ＰＤＦカードＮｏ．１０－０１７３）、ＡｌＮ（ＰＤＦカードＮｏ．２５－１１３３）、ｃＢＮ（ＰＤＦカードＮｏ．３５－１３６５）、Ｃｏ（ＰＤＦカードＮｏ．１５－０８０６）、Ｃｏ5.47Ｎ（ＰＤＦカードＮｏ．４１－０９４３）、Ｃｒ（ＰＤＦカードＮｏ．０６－０６９４）、ＣｒＮ（ＰＤＦカードＮｏ．１１－００６５）、Ｃｒ2Ｎ（ＰＤＦカードＮｏ．３５－０８０３）、Ｃｒ3Ｃ2（ＰＤＦカードＮｏ．３５－０８０４）、Ｍｏ2Ｃ（ＰＤＦカードＮｏ．３５－０７８７）、ＴｉＮ（ＰＤＦカードＮｏ．３８－１４２０）、ＶＣ（ＰＤＦカードＮｏ．３５－０７８６）、ＷＣ（ＰＤＦカードＮｏ．５１－０９３９）、ＷＢ（ＰＤＦカードＮｏ．０６－０５４１）など）を同定した。それらの結果を表２に示す。
Figure JPOXMLDOC01-appb-T000002
　発明品および比較品について、立方晶窒化硼素焼結体をレーザーカット加工機で、所定の形状にカットして超硬合金基材にろう付けし、研削仕上げ加工をしてＩＳＯ規格ＣＮＧＡ１２０４０８切削インサート形状の切削工具を得た。これらの切削インサートを用いて、下記の切削試験（１）および（２）を行った。それらの結果を表３に示す。
切削試験（１）
外周連続湿式切削（旋削）、
被削材：浸炭焼入れした焼結金属（化学成分　Ｃ：０．２～１．０質量％，Ｆｅ：残部，その他：１質量％以下（旧ＪＩＳ規格ＳＭＦ４０４０相当）、ＨＲＡ６３～６５）、
被削材形状：円柱φ４５ｍｍ×８５ｍｍ、
切削速度：２５０ｍ／ｍｉｎ、
切込み量：０．２ｍｍ、
送り：０．１ｍｍ／ｒｅｖ、
インサート形状：ＣＮＧＡ１２０４０８、
ホルダー：ＤＣＬＮＲ２５２５Ｍ１２、
評価：コーナ摩耗量ＶＢｃが０．１５ｍｍに達するまでの切削時間あるいは欠損までの切削時間。
切削試験（２）
外周断続湿式切削（旋削）、
被削材：焼結金属（化学成分　Ｃ：０．２～１．０質量％，Ｆｅ：残部，その他：１質量％以下（旧ＪＩＳ規格ＳＭＦ４０４０相当）、ＨＲＢ７７～８０）、
被削材形状：ギア形状φ４５ｍｍ（歯高８ｍｍ）×３０ｍｍ、
切削速度：３００ｍ／ｍｉｎ、
切込み量：０．２ｍｍ、
送り：０．１ｍｍ／ｒｅｖ、
インサート形状：ＣＮＧＡ１２０４０８、
ホルダー：ＤＣＬＮＲ２５２５Ｍ１２、
評価：コーナ摩耗量ＶＢｃが０．１５ｍｍに達するまでの切削時間あるいは欠損までの切削時間。
Figure JPOXMLDOC01-appb-T000003
　表３に示されるように、本発明の立方晶窒化硼素焼結体は耐摩耗性および耐欠損性に優れるため、比較の立方晶窒化硼素焼結体よりも工具寿命が長いことがわかる。
［実施例２］
　実施例１の原料粉末を表４に示す配合組成に配合し、実施例１と同様の製造方法により立方晶窒化硼素焼結体を作製した。
Figure JPOXMLDOC01-appb-T000004
　得られた立方晶窒化硼素焼結体について、実施例１と同様の測定方法により各種測定を行った。それらの結果を表５に示す。
Figure JPOXMLDOC01-appb-T000005
　発明品および比較品について、実施例１と同様な方法で立方晶窒化硼素焼結体を加工して、ＩＳＯ規格ＣＮＧＡ１２０４０８切削インサート形状の切削工具を得た。これらの切削インサートを用いて、実施例１と同じ試験条件の切削試験（１）および（２）を行った。それらの結果を表６に示す。
Figure JPOXMLDOC01-appb-T000006
　表６に示されるように、本発明の立方晶窒化硼素焼結体は耐摩耗性および耐欠損性に優れるため、比較の立方晶窒化硼素焼結体よりも工具寿命が長いことがわかる。
［実施例３］
　実施例１の原料粉末を表７に示す配合組成に配合し、実施例１と同様の製造方法により立方晶窒化硼素焼結体を作製した。
Figure JPOXMLDOC01-appb-T000007
　得られた立方晶窒化硼素焼結体について、実施例１と同様の測定方法により各種測定を行った。それらの結果を表８に示す。
Figure JPOXMLDOC01-appb-T000008
　発明品および比較品について、実施例１と同様な方法で立方晶窒化硼素焼結体を加工して、ＩＳＯ規格ＣＮＧＡ１２０４０８切削インサート形状の切削工具を得た。これらの切削インサートを用いて、実施例１と同じ試験条件の切削試験（１）および（２）を行った。それらの結果を表９に示す。
Figure JPOXMLDOC01-appb-T000009
　表９に示されるように、本発明の立方晶窒化硼素焼結体は耐摩耗性および耐欠損性に優れるため、比較の立方晶窒化硼素焼結体よりも工具寿命が長いことがわかる。
［実施例４］
　実施例１の発明品１の表面にＰＶＤ装置を用いて被覆処理を行った。発明品１の表面に平均膜厚３μｍのＴｉＮ膜を形成したものを発明品１７、発明品１の表面に平均膜厚３μｍのＴｉＡｌＮ膜を形成したものを発明品１８とした。発明品１７、１８について実施例１と同じ切削試験（１）および（２）を行った。それらの結果を表１０に示す。
Figure JPOXMLDOC01-appb-T000010
　被膜を形成した発明品１７、１８は、被膜を形成していない発明品１よりも工具寿命をさらに長くすることができた。
　本発明によれば、耐摩耗性、耐欠損性および靭性に優れた立方晶窒化硼素焼結体および被覆立方晶窒化硼素焼結体を提供することができる。本発明の立方晶窒化硼素焼結体および被覆立方晶窒化硼素焼結体を切削工具や耐摩耗工具として使用した場合、工具寿命を延長することができるという効果が得られる。

Claims (13)

  1. 　立方晶窒化硼素：８５～９５体積％と、結合相および不可避的不純物：５～１５体積％とから構成され、結合相は、Ａｌ、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから成る群より選択された元素の炭化物、窒化物、炭窒化物、酸化物およびこれらの相互固溶体から成る群より選択された３種以上の化合物とからなり、立方晶窒化硼素焼結体に含まれるアルミニウム元素量は立方晶窒化硼素焼結体の全質量に対して０．５～５質量％であり、但し、結合相中に金属単体および合金は含まれないことを特徴とする立方晶窒化硼素焼結体。
  2. 　結合相は、ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種の化合物と、Ｖ、Ｃｒ、Ｍｎ、Ｃｏ、Ｎｉ、ＮｂおよびＭｏから成る群より選択された元素の炭化物、窒化物、炭窒化物およびこれらの相互固溶体から成る群より選択された２種以上の化合物とからなる請求項１に記載の立方晶窒化硼素焼結体。
  3. 　結合相は、ＡｌＮおよびＡｌ2Ｏ3の少なくとも１種の化合物と、Ｃｏ5.47Ｎ、Ｃｒ2Ｎ、ＣｒＮ、Ｃｒ3Ｃ2、Ｍｏ2ＣおよびＶＣから成る群より選択された２種以上の化合物とからなる請求項１または２に記載の立方晶窒化硼素焼結体。
  4. 　結合相は、少なくともＣｏ5.47ＮおよびＣｒ2Ｎを含有する請求項１～３のいずれか１項に記載の立方晶窒化硼素焼結体。
  5. 　結合相は、Ａｌ2Ｏ3とＡｌＮとＣｏ5.47ＮとＣｒ2Ｎとからなる請求項１～４のいずれか１項に記載の立方晶窒化硼素焼結体。
  6. 　立方晶窒化硼素焼結体に含まれるタングステン元素量は、立方晶窒化硼素焼結体の全質量に対して５質量％以下である請求項１～５のいずれか１項に記載の立方晶窒化硼素焼結体。
  7. 　結合相中に含まれない金属単体および合金は、金属単体が１種の金属元素から構成される金属であり、合金が２種以上の金属元素から構成される金属である請求項１～６のいずれか１項に記載の被覆立方晶窒化硼素焼結体。
  8. 　切削工具または耐摩耗工具として使用される請求項１～７のいずれか１項に記載の立方晶窒化硼素焼結体。
  9. 　請求項１～７のいずれか１項に記載の立方晶窒化硼素焼結体の表面に被膜を形成した被覆立方晶窒化硼素焼結体。
  10. 　被膜がＴｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗ、ＡｌおよびＳｉから成る群より選択された少なくとも１種の金属、これら金属の少なくとも１種の酸化物、炭化物、窒化物、硼化物およびこれらの相互固溶体から成る群より選択された少なくとも１種からなる請求項９に記載の被覆立方晶窒化硼素焼結体。
  11. 　被膜がＴｉＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＡｌＮ、ＴｉＳｉＮおよびＣｒＡｌＮから成る群より選択された少なくとも１種からなる請求項９または１０に記載の被覆立方晶窒化硼素焼結体。
  12. 　被膜の平均膜厚が、０．５～１５μｍである請求項９～１１のいずれか１項に記載の被覆立方晶窒化硼素焼結体。
  13. 　切削工具または耐摩耗工具として使用される請求項９～１２のいずれか１項に記載の被覆立方晶窒化硼素焼結体。
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US9327352B2 (en) 2016-05-03

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