JP6330387B2 - Sintered body and manufacturing method thereof - Google Patents
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- 238000004519 manufacturing process Methods 0.000 title claims description 8
- 239000002245 particle Substances 0.000 claims description 72
- 229910052720 vanadium Inorganic materials 0.000 claims description 41
- 229910052782 aluminium Inorganic materials 0.000 claims description 37
- 229910052751 metal Inorganic materials 0.000 claims description 36
- 239000002184 metal Substances 0.000 claims description 36
- 229910052719 titanium Inorganic materials 0.000 claims description 35
- 229910052759 nickel Inorganic materials 0.000 claims description 34
- 229910052721 tungsten Inorganic materials 0.000 claims description 34
- 229910000765 intermetallic Inorganic materials 0.000 claims description 21
- 230000032683 aging Effects 0.000 claims description 15
- 239000000843 powder Substances 0.000 claims description 15
- 229910052804 chromium Inorganic materials 0.000 claims description 13
- -1 TiCN Inorganic materials 0.000 claims description 11
- 238000005728 strengthening Methods 0.000 claims description 11
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 10
- 238000005245 sintering Methods 0.000 claims description 10
- 229910018072 Al 2 O 3 Inorganic materials 0.000 claims description 9
- 229910017109 AlON Inorganic materials 0.000 claims description 8
- 229910052582 BN Inorganic materials 0.000 claims description 8
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims description 8
- 229910003564 SiAlON Inorganic materials 0.000 claims description 8
- 229910003460 diamond Inorganic materials 0.000 claims description 8
- 239000010432 diamond Substances 0.000 claims description 8
- 239000011812 mixed powder Substances 0.000 claims description 8
- 229910052750 molybdenum Inorganic materials 0.000 claims description 8
- 238000001556 precipitation Methods 0.000 claims description 8
- 229910052726 zirconium Inorganic materials 0.000 claims description 8
- 239000013078 crystal Substances 0.000 claims description 7
- 229910034327 TiC Inorganic materials 0.000 claims description 6
- 239000011159 matrix material Substances 0.000 claims description 5
- 238000002156 mixing Methods 0.000 claims description 3
- 230000002194 synthesizing effect Effects 0.000 claims description 2
- 230000002787 reinforcement Effects 0.000 claims 1
- 238000005520 cutting process Methods 0.000 description 45
- 239000010936 titanium Substances 0.000 description 36
- 239000000463 material Substances 0.000 description 16
- 230000000052 comparative effect Effects 0.000 description 10
- 230000003014 reinforcing effect Effects 0.000 description 9
- 239000011324 bead Substances 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 7
- 239000000956 alloy Substances 0.000 description 7
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 239000000203 mixture Substances 0.000 description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 229910010037 TiAlN Inorganic materials 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 239000002002 slurry Substances 0.000 description 4
- 229910000760 Hardened steel Inorganic materials 0.000 description 3
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 3
- 229910052796 boron Inorganic materials 0.000 description 3
- 239000010730 cutting oil Substances 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 229910001026 inconel Inorganic materials 0.000 description 3
- 238000005259 measurement Methods 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910052581 Si3N4 Inorganic materials 0.000 description 2
- JXOOCQBAIRXOGG-UHFFFAOYSA-N [B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[Al] Chemical compound [B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[B].[Al] JXOOCQBAIRXOGG-UHFFFAOYSA-N 0.000 description 2
- 239000012300 argon atmosphere Substances 0.000 description 2
- 239000002775 capsule Substances 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 238000006555 catalytic reaction Methods 0.000 description 2
- 239000011195 cermet Substances 0.000 description 2
- 239000002612 dispersion medium Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 239000012299 nitrogen atmosphere Substances 0.000 description 2
- 230000000704 physical effect Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 description 2
- 229910052715 tantalum Inorganic materials 0.000 description 2
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- 101000912561 Bos taurus Fibrinogen gamma-B chain Proteins 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- 229910001208 Crucible steel Inorganic materials 0.000 description 1
- 229910002796 Si–Al Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 238000003483 aging Methods 0.000 description 1
- 238000000889 atomisation Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 229910002091 carbon monoxide Inorganic materials 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 238000007542 hardness measurement Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 239000004570 mortar (masonry) Substances 0.000 description 1
- 229910052758 niobium Inorganic materials 0.000 description 1
- 238000009832 plasma treatment Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 description 1
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Manufacture Of Metal Powder And Suspensions Thereof (AREA)
- Powder Metallurgy (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
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Description
本発明は、焼結体およびその製造方法に関する。 The present invention relates to a sintered body and a method for producing the same.
切削加工などに用いられる切削工具の材料として、炭化タングステン（ＷＣ）や立法晶窒化ホウ素（ｃＢＮ）などの硬質粒子をＣｏやＮｉを主体とした金属で結合した焼結体が市販されている。これらの焼結体は、耐欠損性は高いものの、結合金属相が高温で軟化するため、切削工具として使用した場合、耐摩耗性が低下したり、被削材金属が工具に溶着して工具が損傷するなどの問題があった。特に近年は、耐熱合金など、難削材に対する切削工具性能の向上の要求が強まっている。 As a material for a cutting tool used for cutting or the like, a sintered body in which hard particles such as tungsten carbide (WC) and cubic boron nitride (cBN) are bonded with a metal mainly containing Co or Ni is commercially available. Although these sintered bodies have high fracture resistance, the bonded metal phase softens at high temperatures, so when used as a cutting tool, the wear resistance decreases or the work material metal is welded to the tool and the tool There were problems such as damage. Particularly in recent years, there has been an increasing demand for improvement of cutting tool performance for difficult-to-cut materials such as heat-resistant alloys.
ｃＢＮやサーメットなどの焼結体の切削性能を改善するために、ＴｉＮやＡｌ２Ｏ３などのコーティングが行われてきた（特許文献１：特開昭５９−８６７９号公報）。 In order to improve the cutting performance of sintered bodies such as cBN and cermet, coatings such as TiN and Al 2 O 3 have been performed (Patent Document 1: JP 59-8679 A).
しかし、高温での硬度の維持と耐欠損性を十分に維持することは困難であった。特に近年は、耐熱合金など、難削材に対する切削工具性能の向上の要求が強まっている。 However, it has been difficult to maintain sufficient hardness at a high temperature and to maintain sufficient fracture resistance. Particularly in recent years, there has been an increasing demand for improvement of cutting tool performance for difficult-to-cut materials such as heat-resistant alloys.
上記の事情に鑑みて、本発明は、工具材料として用いた場合に、優れた高温硬度と耐欠損性とを有する焼結体およびその製造方法を提供することを目的とする。 In view of the above circumstances, an object of the present invention is to provide a sintered body having excellent high-temperature hardness and fracture resistance when used as a tool material, and a method for producing the same.
本願１の発明は、
（１）硬質粒子として立方晶窒化ホウ素（ｃＢＮ）、Ａｌ２Ｏ３、ＡｌＯＮ、ＳｉＡｌＯＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＮ、ＷＣおよびダイヤモンドからなる群から選択される１種類以上よりなる硬質粒子と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）で表される金属相とを含むことを特徴とする焼結体である。
The invention of this application 1
(1) Hard particles composed of one or more kinds selected from the group consisting of cubic boron nitride (cBN), Al 2 O 3 , AlON, SiAlON, TiC, TiCN, TiN, WC and diamond as hard particles; , Ni) 3 (Al, W, V, Ti), and a sintered body characterized by including a metal phase.
本発明によれば、工具材料として用いた場合に、優れた高温硬度と耐欠損性を有する焼結体を得ることができる。 According to the present invention, when used as a tool material, a sintered body having excellent high temperature hardness and fracture resistance can be obtained.
［本願発明の実施形態の説明］
最初に本願発明の実施形態の内容を列記して説明する。
[Description of Embodiment of Present Invention]
First, the contents of the embodiments of the present invention will be listed and described.
本願の実施形態に係る発明は、（１）硬質粒子として立方晶窒化ホウ素（ｃＢＮ）、Ａｌ２Ｏ３、ＡｌＯＮ、ＳｉＡｌＯＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＮ、ＷＣおよびダイヤモンドからなる群から選択される１種類以上よりなる硬質粒子と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）で表される金属相とを含むことを特徴とする焼結体である。このような焼結体は、工具材料として用いた場合に、優れた高温硬度と耐欠損性を有する。 The invention according to the embodiment of the present application is (1) one type selected from the group consisting of cubic boron nitride (cBN), Al 2 O 3 , AlON, SiAlON, TiC, TiCN, TiN, WC and diamond as hard particles. It is a sintered body characterized by including hard particles composed of the above and a metal phase represented by (Co, Ni) 3 (Al, W, V, Ti). Such a sintered body has excellent high-temperature hardness and fracture resistance when used as a tool material.
（２）前記硬質粒子と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の金属相との両者は、焼結体中に分散された状態で含まれることが好ましい。これにより、高温硬度と耐欠損性を両立させた焼結体を得ることができる。 (2) It is preferable that both the hard particles and the metal phase of (Co, Ni) 3 (Al, W, V, Ti) are contained in a dispersed state in the sintered body. Thereby, the sintered compact which made high temperature hardness and defect resistance compatible can be obtained.
（３）前記金属相中において、Ｃｏの含有率が０〜９０質量％であり、Ｎｉの含有率が０〜９０質量％であり、Ａｌの含有率が０．１〜１５質量％であり、Ｗの含有率が０〜４５質量％であり、Ｖの含有量が０〜２５質量％であり、Ｔｉの含有率が０〜２５質量％であり、Ａｌ、Ｗ、ＶおよびＴｉの合計量の比率が５０質量％以下であることが好ましい。これにより、時効処理後に高温硬度の高い強化相（（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の析出相）が析出し、焼結体の高温硬度を上げることができる。 (3) In the metal phase, the Co content is 0 to 90 mass%, the Ni content is 0 to 90 mass%, and the Al content is 0.1 to 15 mass%, The W content is 0 to 45% by mass, the V content is 0 to 25% by mass, the Ti content is 0 to 25% by mass, and the total content of Al, W, V and Ti is The ratio is preferably 50% by mass or less. Thereby, the strengthening phase (precipitation phase of (Co, Ni) 3 (Al, W, V, Ti)) having a high temperature hardness is precipitated after the aging treatment, and the high temperature hardness of the sintered body can be increased.
（４）前記金属相が、ＣｏおよびＮｉからなるマトリックス相であるγ相と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の析出相である強化相とを含むことが好ましい。これにより、焼結体の高温硬度を上げることができる。ここで強化相とは、Ｎｉ３Ａｌなどに代表されるＬ１２構造（γ’相）、Ｎｉ３Ｖなどに代表されるＤ０２２相（γ”相）、Ｎｉ３Ｔｉなどに代表されるＤ０２４構造など、優れた高温強度特性を持つ析出相のことである。 (4) It is preferable that the metal phase includes a γ phase that is a matrix phase composed of Co and Ni and a strengthening phase that is a precipitated phase of (Co, Ni) 3 (Al, W, V, Ti). Thereby, the high temperature hardness of a sintered compact can be raised. Here reinforcing phase A, L1 2 structure (gamma 'phase) typified by Ni 3 Al, D0 22 phase typified Ni 3 V (γ "phase), typified by Ni 3 Ti D0 It is a precipitated phase having excellent high temperature strength characteristics such as 24 structure.
（５）前記強化相の平均結晶粒径は、３０〜１０００ｎｍであることが好ましい。この範囲である場合、得られる焼結体の高温硬度がより高くなるからである。 (5) The average crystal grain size of the reinforcing phase is preferably 30 to 1000 nm. This is because the high-temperature hardness of the obtained sintered body becomes higher in this range.
（６）前記硬質粒子の平均粒径が０．１〜１０μｍであり、焼結体中の前記硬質粒子の含有率が５０〜９９体積％であることが好ましい。このような粒径範囲と組成範囲である場合、得られる焼結体の硬度がより高くなるからである。 (6) It is preferable that the average particle diameter of the said hard particle is 0.1-10 micrometers, and the content rate of the said hard particle in a sintered compact is 50-99 volume%. This is because the hardness of the obtained sintered body is higher when the particle diameter is within such a range and composition range.
（７）前記硬質粒子にｃＢＮを含む場合に、前記金属相中のＣｒ、Ｍｏ、ＶおよびＺｒのそれぞれの含有量は０．１質量％以下であることが好ましい。Ｃｒ、Ｍｏ、Ｖ、Ｚｒのいずれかの添加量が０．１質量％を超えると、Ｃｒ、Ｍｏ、ＶおよびＺｒの触媒反応により、時効処理の際にｃＢＮが柔らかい六方晶窒化ホウ素（ｈＢＮ）に変化してしまう畏れがあるためである。 (7) When cBN is contained in the hard particles, the contents of Cr, Mo, V and Zr in the metal phase are preferably 0.1% by mass or less. When the added amount of any of Cr, Mo, V, and Zr exceeds 0.1% by mass, hexagonal boron nitride (hBN) having a soft cBN during aging treatment is caused by the catalytic reaction of Cr, Mo, V, and Zr. This is because there is a fear of changing.
（８）本発明は、上記の焼結体の製造方法であって、Ｃｏ、Ｎｉ、Ａｌ、Ｗ、ＶおよびＴｉを含む金属間化合物を合成する工程と、前記金属間化合物を粉砕して、金属間化合物粉末を得る工程と、前記金属間化合物粉末と前記硬質粒子の粉末とを混合して、混合粉末を得る工程と、前記混合粉末を１０ＭＰａ〜１６ＧＰａ、１０００〜１８００℃の条件で焼結する工程と、焼結後に５００〜１１００℃で時効処理を行う工程とを含む、製造方法にも関する。１０ＭＰａ〜１６ＧＰａの圧力と、１０００〜１８００℃の温度で焼結することにより、硬質粒子と金属間化合物の緻密な焼結体を形成できる。また、時効化処理を行うことにより、γ相（高靭性のＣｏおよびＮｉからなるマトリクス相）中に高温硬度の高い強化相（（Ｃｏ、Ｎｉ）３（Ａｌ、Ｗ、Ｖ、Ｔｉ）の析出相）が形成され、高温硬度の高い焼結体を形成することができる。 (8) The present invention is a method for producing the above sintered body, comprising a step of synthesizing an intermetallic compound containing Co, Ni, Al, W, V and Ti, and pulverizing the intermetallic compound. A step of obtaining an intermetallic compound powder, a step of mixing the intermetallic compound powder and the powder of the hard particles to obtain a mixed powder, and sintering the mixed powder under conditions of 10 MPa to 16 GPa and 1000 to 1800 ° C. And a manufacturing method including a step of performing an aging treatment at 500 to 1100 ° C. after sintering. By sintering at a pressure of 10 MPa to 16 GPa and a temperature of 1000 to 1800 ° C., a dense sintered body of hard particles and an intermetallic compound can be formed. Further, by performing an aging treatment, precipitation of a strengthening phase ((Co, Ni) 3 (Al, W, V, Ti) having a high temperature hardness in a γ phase (a matrix phase composed of highly tough Co and Ni). Phase) is formed, and a sintered body having high high-temperature hardness can be formed.
［本願発明の実施形態の詳細］
本発明の焼結体は、立方晶窒化ホウ素、Ａｌ２Ｏ３、ＡｌＯＮ、ＳｉＡｌＯＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＮ、ＷＣおよびダイヤモンドからなる群から選択される１種類以上よりなる硬質粒子と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）で表される金属相とを含むことを特徴とする。（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の金属相とは、ＣｏおよびＮｉの合計と、Ａｌ，Ｗ，ＶおよびＴｉの合計との比が３：１となるような元素比率組成を主として構成される、強化相を意味する。ここで、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）と表現しているが、強化相として最適な金属相を示しているのであり、このうちＣｏ，Ｗ，Ｖ，Ｔｉについては含有しなくても良い。
[Details of the embodiment of the present invention]
The sintered body according to the present invention includes one or more hard particles selected from the group consisting of cubic boron nitride, Al 2 O 3 , AlON, SiAlON, TiC, TiCN, TiN, WC and diamond, and (Co, And a metal phase represented by Ni) 3 (Al, W, V, Ti). The metal phase of (Co, Ni) 3 (Al, W, V, Ti) is an element ratio such that the ratio of the sum of Co and Ni to the sum of Al, W, V and Ti is 3: 1. It means a reinforcing phase mainly composed of a composition. Here, it is expressed as (Co, Ni) 3 (Al, W, V, Ti), but shows an optimum metal phase as a strengthening phase. Among these, Co, W, V, Ti It does not need to contain.
前記硬質粒子と、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の金属相との両者は、ＣｏおよびＮｉからなるマトリックス相であるγ相と共に焼結体中に分散された状態で含まれることが好ましい。これにより、高温硬度と耐欠損性を両立させた焼結体を得ることができる。両者は、焼結体中に均一に分散された状態で含まれていることが、より好ましい。 Both the hard particles and the metal phase of (Co, Ni) 3 (Al, W, V, Ti) are dispersed in the sintered body together with the γ phase which is a matrix phase composed of Co and Ni. It is preferably included. 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.
本発明の一実施の形態においては、まず、Ｃｏ、Ｎｉ、Ａｌ、Ｗ、ＶおよびＴｉを原料として使用し、アトマイズ、アーク溶解、またはプラズマ処理などにより、金属間化合物を作製する。この金属間化合物を用いて、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の金属相が構成される。 In one embodiment of the present invention, first, an intermetallic compound is produced by using atomization, arc melting, plasma treatment or the like using Co, Ni, Al, W, V and Ti as raw materials. Using this intermetallic compound, a metal phase of (Co, Ni) 3 (Al, W, V, Ti) is formed.
（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の金属相の全量に対して、Ｃｏの含有率が０〜９０質量％であり、Ｎｉの含有率が０〜９０質量％であり、Ａｌの含有率が０．１〜１５質量％であり、Ｗの含有率が０〜４５質量％であり、Ｖの含有量が０〜２５質量％であり、Ｔｉの含有率が０〜２５質量％であり、Ａｌ、Ｗ、ＶおよびＴｉの合計量の比率が５０質量％以下であることが好ましい。これにより、時効処理後に高温硬度の高い強化相（（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）の析出相）が析出し、焼結体の高温硬度を上げることができる。より好ましくは、Ｃｏの含有率が１〜５０質量％、Ｎｉの含有率が１〜５０質量％、Ａｌの含有率が０．１〜１０質量％、Ｗの含有率が３〜４５質量％の組成である。 The Co content is 0 to 90% by mass and the Ni content is 0 to 90% by mass with respect to the total amount of the metal phase of (Co, Ni) 3 (Al, W, V, Ti), The Al content is 0.1 to 15% by mass, the W content is 0 to 45% by mass, the V content is 0 to 25% by mass, and the Ti content is 0 to 25% by mass. %, And the ratio of the total amount of Al, W, V and Ti is preferably 50% by mass or less. Thereby, the strengthening phase (precipitation phase of (Co, Ni) 3 (Al, W, V, Ti)) having a high temperature hardness is precipitated after the aging treatment, and the high temperature hardness of the sintered body can be increased. More preferably, the Co content is 1 to 50 mass%, the Ni content is 1 to 50 mass%, the Al content is 0.1 to 10 mass%, and the W content is 3 to 45 mass%. Composition.
なお、金属間化合物粉末を作製する際には、Ｃｏ、Ｎｉ、Ａｌ、Ｗ、ＶおよびＴｉ以外に、Ｎｂ、Ｔａ、Ｂ、Ｃなどを添加しても良い。ただし、硬質粒子にｃＢＮを用いる場合、金属相の全量に対するＣｒ、Ｍｏ、Ｖ、Ｚｒのそれぞれの添加量は０．１質量％以下とすることが好ましい。Ｃｒ、Ｍｏ、Ｖ、Ｚｒのいずれかの添加量が０．１質量％を超えると、Ｃｒ、Ｍｏ、ＶおよびＺｒの触媒反応により、時効処理の際にｃＢＮが柔らかい六方晶窒化ホウ素（ｈＢＮ）に変化してしまう畏れがあるためである。ここで、時効処理（時効硬化処理、析出熱処理）とは、硬さ、強さ又は耐食性などを増進させるために適切な温度、又はある種類の合金や質別に対しては室温で、溶体化処理（固溶化熱処理）した製品を均熱保持する処理（ＪＩＳ Ｗ １１０３ 参照）を意味する。 In addition, when producing intermetallic compound powder, Nb, Ta, B, C, etc. may be added in addition to Co, Ni, Al, W, V and Ti. However, when cBN is used for the hard particles, the addition amount of Cr, Mo, V, and Zr with respect to the total amount of the metal phase is preferably 0.1% by mass or less. When the added amount of any of Cr, Mo, V, and Zr exceeds 0.1% by mass, hexagonal boron nitride (hBN) having a soft cBN during aging treatment is caused by the catalytic reaction of Cr, Mo, V, and Zr. This is because there is a fear of changing. Here, aging treatment (age hardening treatment, precipitation heat treatment) is a solution treatment at a temperature suitable for increasing hardness, strength, corrosion resistance, etc., or at a room temperature for a certain type of alloy or quality. (Solution heat treatment) This means a treatment (see JIS W 1103) for keeping the product soaked.
また、前記硬質粒子にｃＢＮを用いる場合には、前記強化相が硬質粒子周辺において高いＢ濃度を含有することが好ましい。 In addition, when cBN is used for the hard particles, the reinforcing phase preferably contains a high B concentration around the hard particles.
また、前記硬質粒子にＡｌ２Ｏ３，ＡｌＯＮ，ＳｉＡｌＯＮを用いる場合には、前記強化相が硬質粒子周辺においてその他の領域より高いＡｌ濃度を含有することが好ましい。 Further, when Al 2 O 3 , AlON, or SiAlON is used for the hard particles, it is preferable that the strengthening phase contains an Al concentration higher than other regions around the hard particles.
また、前記硬質粒子にＴｉＣ，ＴｉＣＮ，ＴｉＮを用いる場合には、前記強化相が硬質粒子周辺においてその他の領域より高いＴｉ濃度を含有することが好ましい。 In addition, when TiC, TiCN, or TiN is used for the hard particles, it is preferable that the reinforcing phase contains a higher Ti concentration in the periphery of the hard particles than in other regions.
また、前記硬質粒子にＷＣを用いる場合には、前記強化相が硬質粒子周辺においてその他の領域より高いＷ濃度を含有することが好ましい。 Moreover, when using WC for the hard particles, it is preferable that the reinforcing phase contains a higher W concentration than the other regions around the hard particles.
また、硬質粒子として上記以外に、ＴｉＡｌＮ、ＡｌＣｒＮなどを用いても良い。ＴｉＡｌＮの場合は、前記強化相が硬質粒子周辺において他の領域より高いＡｌ、Ｔｉ濃度を含有することが好ましい。ＡｌＣｒＮの場合は、前記強化相が硬質粒子周辺において他の領域より高いＡｌ、Ｃｒ濃度を含有し、（Ｃｏ，Ｎｉ，Ｃｒ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）を形成することが好ましい。 In addition to the above, TiAlN, AlCrN, or the like may be used as the hard particles. In the case of TiAlN, it is preferable that the strengthening phase contains Al and Ti concentrations higher than other regions around the hard particles. In the case of AlCrN, it is preferable that the reinforcing phase contains Al and Cr concentrations higher than other regions around the hard particles to form (Co, Ni, Cr) 3 (Al, W, V, Ti).
さらに、焼結プロセスもしくは時効化処理プロセスによって、焼結体中にＮｉ２０Ａｌ３Ｂ６などに代表される金属のアルミホウ化物を生成しても良い。このようなアルミホウ化物を形成することにより、金属相とｃＢＮとの結合力が強化され、耐欠損性の優れた焼結体が得られる。 Furthermore, a metal aluminum boride typified by Ni 20 Al 3 B 6 or the like may be generated in the sintered body by a sintering process or an aging treatment process. By forming such an aluminum boride, the bonding strength between the metal phase and cBN is strengthened, and a sintered body having excellent fracture resistance is obtained.
得られた金属間化合物は、例えばビーズミルやボールミル、ジェットミルなどによって粉砕されて、金属間化合物粉末となる。金属間化合物粉末の平均粒径は、０．３〜３μｍであることが好ましい。ビーズミル／ボールミルに用いるビーズ／ボールとしては、例えば粒径０．１〜３ｍｍのアルミナ製、窒化ケイ素製、超硬合金製ビーズ／ボールが挙げられ、分散媒としては、例えばエタノールやアセトン、液体窒素が挙げられる。ビーズミル／ボールミルによる処理時間は、例えば３０分〜１０時間である。ビーズミル／ボールミルにより得られたスラリーは、例えばＮ２中で乾燥させる。 The obtained intermetallic compound is pulverized by, for example, a bead mill, a ball mill, a jet mill or the like to form an intermetallic compound powder. The average particle size of the intermetallic compound powder is preferably 0.3 to 3 μm. Examples of the beads / balls used for the bead mill / ball mill include alumina, silicon nitride, and cemented carbide beads / balls having a particle diameter of 0.1 to 3 mm. Examples of 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 10 hours. The slurry obtained by the bead mill / ball mill is dried, for example, in N 2 .
次に、得られた金属間化合物粉末と硬質粒子粉末を、ボールミルや乳鉢等によって混合する。ｃＢＮは極めて硬度が高く、工具として高い切削性能を示す。また、Ａｌ２Ｏ３、ＡｌＯＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＮ、ＴｉＡｌＮ、ＡｌＣｒＮはＦｅに対して反応摩耗しにくい物性を持っているため、Ｆｅを含む鋳鉄、鋼、焼入鋼などの被削材に好適である。また、ＳｉＡｌＯＮ（α、β、立方晶のいずれの結晶構造も含む）はＮｉに対して反応摩耗しにくい物性を持っているため、インコネルなど耐熱合金に好適である。またこれらの硬質粒子に加えて、Ｍｏ２Ｃ、Ｃｒ３Ｃ２、ＴａＣ、ＮｂＣ、ＶＣ、ＨｆＣ、ＺｒＣ、ＡｌＮ、ＣｒＮ、ＴａＮ、ＮｂＮ、ＶＮ、ＨｆＮ、ＺｒＮなどの硬質粒子を添加しても良い。なお、ＴｉＣ、ＴｉＣＮ、ＴｉＮを硬質粒子として用いる場合は、ＣｏよりＮｉが多い方が硬質粒子と金属結合材との結合力が強くなり、耐欠損性が増加するため望ましい。ボールミルに用いるボールとしては、例えばアルミナ製、窒化ケイ素製もしくは超硬合金製の直径３ｍｍのボールが挙げられ、分散媒としては例えばエタノールやアセトン、液体窒素が挙げられる。処理時間は、例えば３〜２０時間である。混合により得られたスラリーを、例えばＮ２中で乾燥させることにより混合粉末が得られる。 Next, the obtained intermetallic compound powder and hard particle powder are mixed by a ball mill, a mortar or the like. cBN has extremely high hardness and exhibits high cutting performance as a tool. In addition, Al 2 O 3 , AlON, TiC, TiCN, TiN, TiAlN, and AlCrN have physical properties that do not easily react with Fe, so they can be used as work materials such as cast iron, steel, and hardened steel containing Fe. Is preferred. SiAlON (including any crystal structure of α, β, and cubic) is suitable for heat-resistant alloys such as Inconel because it has physical properties that are difficult to react with Ni. In addition to these hard particles, hard particles such as Mo 2 C, Cr 3 C 2 , TaC, NbC, VC, HfC, ZrC, AlN, CrN, TaN, NbN, VN, HfN, and ZrN may be added. good. When TiC, TiCN, or TiN is used as the hard particles, it is preferable that Ni is more than Co because the bonding force between the hard particles and the metal binder is increased and the fracture resistance is increased. 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 slurry obtained by mixing is dried in, for example, N 2 to obtain a mixed powder.
得られた混合粉末を、Ｔａカプセルに入れ、プレスによって焼結体を形成する。圧力は１０ＭＰａ〜１６ＧＰａ、温度は１０００〜１８００℃で焼結することが好ましい。これにより硬質粒子と金属間化合物の緻密な焼結体を形成できる。 The obtained mixed powder is put into a Ta capsule, and a sintered body is formed by pressing. It is preferable to sinter at a pressure of 10 MPa to 16 GPa and a temperature of 1000 to 1800 ° C. Thereby, a dense sintered body of hard particles and an intermetallic compound can be formed.
焼結後に、５００〜１１００℃で１〜２４時間で時効化処理を行う。これにより、γ相（高靭性のＣｏおよびＮｉからなるマトリクス相）中に高温硬度の高い強化相（（Ｃｏ、Ｎｉ）３（Ａｌ、Ｗ、Ｖ、Ｔｉ）の析出相）が形成され、高温硬度の高い焼結体を形成することができる。強化相単体では、粒界脆性を起こしやすい欠点を持っている。 After sintering, an aging treatment is performed at 500 to 1100 ° C. for 1 to 24 hours. Thereby, a strengthening phase (precipitation phase of (Co, Ni) 3 (Al, W, V, Ti)) having a high temperature hardness is formed in the γ phase (matrix phase composed of high toughness Co and Ni), and the high temperature A sintered body having high hardness can be formed. The reinforced phase alone has a defect that easily causes grain boundary brittleness.
しかしながら本発明により、例えばｃＢＮと焼結した状態で時効処理することにより、粒界へのホウ素添加効果が表れ、従来工具と比べてｃＢＮとの焼結体は特に粒界破壊が起こりにくいため、高温硬度と耐欠損性を両立させた焼結体を得ることができる。 However, according to the present invention, for example, by performing an aging treatment in a sintered state with cBN, an effect of adding boron to the grain boundary appears, and the sintered body with cBN is less susceptible to grain boundary fracture than conventional tools. A sintered body having both high-temperature hardness and fracture resistance can be obtained.
また、Ａｌ２Ｏ３、ＡｌＯＮ、ＳｉＡｌＯＮを硬質粒子として用いた場合は、硬質粒子と金属相との間に他の場所より高濃度Ａｌ領域が形成された（Ｃｏ、Ｎｉ）３（Ａｌ、Ｗ，Ｖ，Ｔｉ）の析出相が多数形成されるため、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 When Al 2 O 3 , AlON, or SiAlON is used as the hard particles, a high concentration Al region is formed between the hard particles and the metal phase from other locations (Co, Ni) 3 (Al, W , V, Ti), a large number of precipitated phases are formed, the bonding force between the hard particles and the metal phase is increased, and a sintered body with high fracture resistance can be obtained.
また、ＴｉＣ、ＴｉＣＮ、ＴｉＮを硬質粒子として用いた場合は、硬質粒子と金属相との間に高濃度Ｔｉ領域が形成された（Ｃｏ、Ｎｉ）３（Ａｌ、Ｗ、Ｖ、Ｔｉ）の析出相が形成され、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 Further, when TiC, TiCN, or TiN is used as hard particles, precipitation of (Co, Ni) 3 (Al, W, V, Ti) in which a high concentration Ti region is formed between the hard particles and the metal phase A phase is formed, the bonding strength between the hard particles and the metal phase is increased, and a sintered body having high fracture resistance can be obtained.
また、ＷＣを硬質粒子として用いた場合は、硬質粒子と金属相との間に他の場所より高濃度Ｗ領域が形成された（Ｃｏ、Ｎｉ）３（Ａｌ、Ｗ，Ｖ，Ｔｉ）の析出相が多数形成されるため、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 When WC is used as hard particles, precipitation of (Co, Ni) 3 (Al, W, V, Ti) in which a higher concentration W region is formed between the hard particles and the metal phase than other places. Since a large number of phases are formed, the bonding force between the hard particles and the metal phase is increased, and a sintered body with high fracture resistance can be obtained.
また、ＴｉＡｌＮを硬質粒子として用いた場合は、硬質粒子と金属相との間に他の場所より高いＡｌ、Ｔｉ濃度を含有し、（Ｃｏ，Ｎｉ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）を形成されるため、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 Further, when TiAlN is used as hard particles, it contains higher Al and Ti concentrations than other places between the hard particles and the metal phase, and (Co, Ni) 3 (Al, W, V, Ti) is contained. As a result, the bonding force between the hard particles and the metal phase is increased, and a sintered body having high fracture resistance can be obtained.
また、ＡｌＣｒＮを硬質粒子として用いた場合は、硬質粒子と金属相との間に他の場所より高いＡｌ、Ｃｒ濃度を含有し、（Ｃｏ，Ｎｉ，Ｃｒ）３（Ａｌ，Ｗ，Ｖ，Ｔｉ）を形成されるため、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 Further, when AlCrN is used as hard particles, it contains higher Al and Cr concentrations than other places between the hard particles and the metal phase, and (Co, Ni, Cr) 3 (Al, W, V, Ti ) Is increased, the bonding force between the hard particles and the metal phase is increased, and a sintered body having high fracture resistance can be obtained.
また、ダイヤモンドを硬質粒子として用いた場合は、硬質粒子と金属相との間において、Ｃ濃度が他の場所より高く、（ＣＯ，Ｎｉ）３（Ａｌ，Ｗ，Ｃ）が形成されるため、硬質粒子と金属相の結合力が増加し、耐欠損性の高い焼結体を得ることが出来る。 When diamond is used as the hard particles, the C concentration is higher between the hard particles and the metal phase than other places, and (CO, Ni) 3 (Al, W, C) is formed. The bonding force between the hard particles and the metal phase is increased, and a sintered body having high fracture resistance can be obtained.
強化相の平均結晶粒径は３０〜１０００ｎｍであることが好ましい。この範囲である場合、得られる焼結体の高温硬度がより高くなるからである。 The average crystal grain size of the reinforcing phase is preferably 30 to 1000 nm. This is because the high-temperature hardness of the obtained sintered body becomes higher in this range.
硬質粒子の平均粒径は０．１〜１０μｍであることが好ましく、焼結体中の硬質粒子の含有率は５０〜９９体積％であることが好ましい。このような粒径範囲と組成範囲である場合、得られる焼結体の硬度がより高くなるからである。なお、硬質粒子の平均粒径は、マイクロトラックなどの粒度分布測定機により測定することができる。 The average particle size of the hard particles is preferably 0.1 to 10 μm, and the content of the hard particles in the sintered body is preferably 50 to 99% by volume. This is because the hardness of the obtained sintered body is higher when the particle diameter is within such a range and composition range. The average particle size of the hard particles can be measured with a particle size distribution measuring machine such as Microtrac.
なお、本発明の焼結体は、不可避不純物としてＢ、Ｎ、Ｏ等を本発明の効果を損なわない範囲で含んでいてもよい。 In addition, the sintered compact of this invention may contain B, N, O, etc. as an inevitable impurity in the range which does not impair the effect of this invention.
以下に、本発明を実施例を用いて詳細に説明するが、これらの実施例は例示的なものであり、本発明の範囲はこれに限定されるものではない。 Hereinafter, the present invention will be described in detail with reference to examples. However, these examples are illustrative, and the scope of the present invention is not limited thereto.
［実施例１〜３７］
（粉末の作製）
表１〜４の「金属間化合物組成（体積％）」欄に記載の割合となるようにＣｏ、Ｎｉ、Ａｌ、Ｗ、ＶおよびＴｉを混合し、アトマイズ法により金属間化合物を作製した。これを粒径０．５ｍｍのアルミナビーズを用い、ビーズミルによって粉砕した。得られたスラリーをＮ２雰囲気中で乾燥させ、金属間化合物粉末を得た。
[Examples 1-37]
(Preparation of powder)
Co, Ni, Al, W, V, and Ti were mixed so as to have the ratio described in the “intermetallic compound composition (volume%)” column of Tables 1 to 4, and an intermetallic compound was prepared by an atomizing method. This was ground by a bead mill using alumina beads having a particle diameter of 0.5 mm. The obtained slurry was dried in an N 2 atmosphere to obtain an intermetallic compound powder.
次に、該金属間化合物粉末と表１〜３に記載の硬質粒子粉末とを超硬合金製の直径３ｍｍのボールとエタノールと共にボールミルに投入し、５時間混合した。得られたスラリーをＮ２雰囲気中で乾燥させ、混合粉末を得た。 Next, the intermetallic compound powder and the hard particle powders shown in Tables 1 to 3 were charged into a ball mill together with a 3 mm diameter ball made of cemented carbide and ethanol, and mixed for 5 hours. The obtained slurry was dried in an N 2 atmosphere to obtain a mixed powder.
（焼結体の作製）
次に、得られた混合粉末をタンタル製のカプセルに充填し、プレス機を用いて、表１〜４の「焼結条件」欄に記載の圧力および温度で焼結処理を行い、焼結体を作製した。
(Production of sintered body)
Next, the obtained mixed powder is filled into a tantalum capsule, and using a press machine, a sintering process is performed at the pressure and temperature described in the “sintering conditions” column of Tables 1 to 4 to obtain a sintered body. Was made.
（時効処理）
得られた焼結体をアルゴン雰囲気炉で表１〜４の「時効処理条件」欄に記載の温度と時間で時効処理を行い、強化相を析出させた。
(Aging treatment)
The obtained sintered body was subjected to an aging treatment at the temperature and time described in the “Aging treatment conditions” column of Tables 1 to 4 in an argon atmosphere furnace to precipitate a strengthening phase.
（焼結体の測定）
強化相の平均結晶粒径は、焼結体を研磨した後、ＳＥＭによる撮影像を基にして測定した。具体的には、ＳＥＭ撮影像の測定範囲内にある結晶粒数Ｎを数え、測定範囲の全面積ＡＭを結晶粒数Ｎで除して結晶粒１個あたりの面積Ａｇを求めた。結晶粒の形状を円と仮定して，Ａｇから半径を算出して、その値を平均結晶粒径ｄＡＶＥとした。
(Measurement of sintered body)
The average crystal grain size of the reinforcing phase was measured on the basis of an image taken by SEM after polishing the sintered body. Specifically, it counted grain numbers N that are within the measuring range of the SEM photographic image to determine the area A g of the crystal grains per unit by dividing by the total area A M grain number N of the measurement range. Assuming circular grain shape, to calculate the radius from the A g, and the value as the average crystal grain size d AVE.
また、硬質粒子にｃＢＮ、Ａｌ２Ｏ３、ＡｌＯＮ、ＳｉＡｌＯＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＮまたはＷＣを用いた試料については、常温における焼結体の硬度、および、８００℃における焼結体の硬度（高温硬度）を、アルゴン雰囲気下で、ビッカース硬度計によって測定した。なお、硬質粒子にダイヤモンドを用いた試料については、硬度測定は不可能であった。また、硬質粒子にｃＢＮを用いた試料については、ＸＲＤ強度を測定することにより、時効処理後の際にｃＢＮが低硬度の六方晶窒化ホウ素（ｈＢＮ）に変換されていないことを確認した。 For samples using hard particles of cBN, Al 2 O 3 , AlON, SiAlON, TiC, TiCN, TiN or WC, the hardness of the sintered body at room temperature and the hardness of the sintered body at 800 ° C. (high temperature Hardness) was measured with a Vickers hardness tester under an argon atmosphere. In addition, hardness measurement was impossible for a sample using diamond as the hard particles. Moreover, about the sample which used cBN for the hard particle | grains, it was confirmed by measuring XRD intensity | strength that cBN was not converted into the hexagonal boron nitride (hBN) of low hardness after the aging treatment.
（切削工具の作製）
得られた焼結体を、ワイヤー放電加工により切断して仕上げ加工し、先端ノーズＲ０．８ｍｍの切削工具を作製した。
(Manufacture of cutting tools)
The obtained sintered body was cut and finished by wire electric discharge machining to produce a cutting tool having a tip nose R of 0.8 mm.
比較例１〜４として、表２に示すようにＣｒ、Ｍｏ、Ｖ、Ｚｒ濃度が高いｃＢＮ焼結体を作製し、ＸＲＤ測定と切削工具の作製を行った。また、表２および３に示すように、比較例５として、８０体積％のＷＣ（炭化タングステン）および２０体積％のＣｏからなる超硬合金を、比較例６として、８０体積％のＴｉＣ（炭化チタン）および２０体積％のＮｉからなるサーメットを用いて、上記と同様の切削工具を作製した。また、表４に示すように、比較例７〜８として、９０体積％のダイヤモンドおよび１０体積％のＣｏからなるダイヤモンド焼結体を用いて、上記と同様の切削工具を作製した。 As Comparative Examples 1 to 4, cBN sintered bodies having high Cr, Mo, V, and Zr concentrations were prepared as shown in Table 2, and XRD measurement and cutting tools were prepared. Further, as shown in Tables 2 and 3, as Comparative Example 5, a cemented carbide composed of 80% by volume of WC (tungsten carbide) and 20% by volume of Co was used, and as Comparative Example 6, 80% by volume of TiC (carbonized). A cutting tool similar to the above was prepared using a cermet made of titanium) and 20% by volume of Ni. Further, as shown in Table 4, as Comparative Examples 7 to 8, the same cutting tool as described above was produced using a diamond sintered body composed of 90% by volume of diamond and 10% by volume of Co.
（切削試験１）
得られた切削工具を用いて、実施例１〜２８と比較例１〜５については以下の切削条件でインコネル（登録商標）７１８（商品名、インコネル社製）を被削材としてＮＣ旋盤で切削試験を行い、０．７ｋｍ切削後の各切削工具の逃げ面の摩耗量（μｍ）を測定した。
(Cutting test 1)
Using Examples 1 to 28 and Comparative Examples 1 to 5, the obtained cutting tool was cut with an NC lathe using Inconel (registered trademark) 718 (trade name, manufactured by Inconel) as a work material under the following cutting conditions. A test was performed, and the wear amount (μm) of the flank of each cutting tool after 0.7 km cutting was measured.
切削速度：２００ｍ／ｍｉｎ．
切込み量：０．２ｍｍ
送り量：０．１ｍｍ／ｒｅｖ
切削油：あり
結果を表１および２に示す。
Cutting speed: 200 m / min.
Cutting depth: 0.2mm
Feed amount: 0.1mm / rev
Cutting oil: yes The results are shown in Tables 1 and 2.
（評価結果１）
実施例１〜２８の焼結体および切削工具は、比較例１〜５の焼結体および切削工具よりも、耐熱合金に対する耐摩耗性が優れていた。
(Evaluation result 1)
The sintered bodies and cutting tools of Examples 1 to 28 were superior to the sintered bodies and cutting tools of Comparative Examples 1 to 5 in wear resistance against the heat-resistant alloy.
（切削試験２）
得られた切削工具を用いて、実施例２９〜３７と比較例６については以下の切削条件で焼入鋼ＳＣＭ４１５を被削材としてＮＣ旋盤で切削試験を行い、３．０ｋｍ切削後の各切削工具の逃げ面の摩耗量（μｍ）を測定した。
(Cutting test 2)
Using the obtained cutting tools, Examples 29 to 37 and Comparative Example 6 were subjected to a cutting test with an NC lathe using the hardened steel SCM415 as a work material under the following cutting conditions, and each cutting after 3.0 km cutting The amount of wear (μm) on the flank of the tool was measured.
切削速度：１００ｍ／ｍｉｎ．
切込み量：０．１ｍｍ
送り量：０．１ｍｍ／ｒｅｖ
切削油：あり
結果を表３に示す。
Cutting speed: 100 m / min.
Cutting depth: 0.1 mm
Feed amount: 0.1mm / rev
Cutting oil: yes The results are shown in Table 3.
（評価結果２）
実施例２９〜３７の焼結体および切削工具は、比較例６の焼結体および切削工具よりも、焼入鋼に対する耐摩耗性が優れていた。
(Evaluation result 2)
The sintered bodies and cutting tools of Examples 29 to 37 were superior to the sintered body and cutting tool of Comparative Example 6 in wear resistance against hardened steel.
（切削試験３）
得られた切削工具を用いて、実施例３８〜４７と比較例７〜８については以下の切削条件でアルミニウム合金Ａ３９０（１７％Ｓｉ−Ａｌ合金）を被削材としてＮＣ旋盤で切削試験を行い、５．０ｋｍ切削後の各切削工具の逃げ面の摩耗量（μｍ）を測定した。
(Cutting test 3)
Using the obtained cutting tools, Examples 38 to 47 and Comparative Examples 7 to 8 were subjected to a cutting test on an NC lathe using the aluminum alloy A390 (17% Si-Al alloy) as a work material under the following cutting conditions. The amount of wear (μm) on the flank face of each cutting tool after 5.0 km cutting was measured.
切削速度：５００ｍ／ｍｉｎ．
切込み量：０．５ｍｍ
送り量：０．１２ｍｍ／ｒｅｖ
切削油：あり
結果を表４に示す。
Cutting speed: 500 m / min.
Cutting depth: 0.5mm
Feed amount: 0.12mm / rev
Cutting oil: yes The results are shown in Table 4.
（評価結果３）
実施例３８〜４７の焼結体および切削工具は、比較例７〜８の焼結体および切削工具よりも、アルミニウム合金に対する耐摩耗性が優れていた。
(Evaluation result 3)
The sintered bodies and cutting tools of Examples 38 to 47 were superior in wear resistance to the aluminum alloy than the sintered bodies and cutting tools of Comparative Examples 7 to 8.
今回開示された実施の形態および実施例はすべての点で例示であって制限的なものではないと考えられるべきである。本発明の範囲は上記した説明ではなくて特許請求の範囲によって示され、特許請求の範囲と均等の意味および範囲内でのすべての変更が含まれることが意図される。 It should be understood that the embodiments and examples disclosed herein are illustrative and non-restrictive in every respect. The scope of the present invention is defined by the terms of the claims, rather than the description above, and is intended to include any modifications within the scope and meaning equivalent to the terms of the claims.
本発明による焼結体は、切削工具に広く利用することができ、長距離にわたって、被削材の表面に平滑な切削表面を形成することができる。特に、高温での硬度の高い被削材、耐熱合金からなる被削材、鉄系材料を含む被削材を切削するための切削工具に好適に利用することができる。 The sintered body according to the present invention can be widely used for a cutting tool, and can form a smooth cutting surface on the surface of a work material over a long distance. In particular, it can be suitably used for a cutting tool for cutting a work material having high hardness at high temperatures, a work material made of a heat-resistant alloy, and a work material containing an iron-based material.
Claims (8)
前記金属相中において、Ｃｏの含有率が１〜５０質量％であり、Ｗの含有率が３〜４５質量％である、焼結体。 Hard particles made of one or more kinds selected from the group consisting of cubic boron nitride, Al 2 O 3 , AlON, SiAlON, TiC, TiCN, TiN, WC and diamond, and (Co, Ni) 3 (Al, W, V, and a metallic phase represented by Ti) seen including,
The sintered compact whose Co content rate is 1-50 mass% and whose W content rate is 3-45 mass% in the said metal phase .
前記金属間化合物を粉砕して、金属間化合物粉末を得る工程と、
前記金属間化合物粉末と前記硬質粒子の粉末とを混合して、混合粉末を得る工程と、
前記混合粉末を１０ＭＰａ〜１６ＧＰａ、１０００〜１８００℃の条件で焼結する工程と、
焼結後に５００〜１８００℃で時効処理を行う工程とを含む、
請求項１に記載の焼結体の製造方法。 Synthesizing an intermetallic compound containing Co, Ni, Al, W, V and Ti;
Crushing the intermetallic compound to obtain an intermetallic compound powder;
Mixing the intermetallic compound powder and the hard particle powder to obtain a mixed powder;
Sintering the mixed powder under conditions of 10 MPa to 16 GPa and 1000 to 1800 ° C .;
Aging treatment at 500-1800 ° C. after sintering,
The manufacturing method of the sintered compact of Claim 1.
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