JPS6143306B2 - - Google Patents
Info
- Publication number
- JPS6143306B2 JPS6143306B2 JP53151483A JP15148378A JPS6143306B2 JP S6143306 B2 JPS6143306 B2 JP S6143306B2 JP 53151483 A JP53151483 A JP 53151483A JP 15148378 A JP15148378 A JP 15148378A JP S6143306 B2 JPS6143306 B2 JP S6143306B2
- Authority
- JP
- Japan
- Prior art keywords
- ultra
- diamond
- high pressure
- powder
- cutting
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired
Links
- 239000000463 material Substances 0.000 claims description 35
- 238000005520 cutting process Methods 0.000 claims description 30
- 229910003460 diamond Inorganic materials 0.000 claims description 30
- 239000010432 diamond Substances 0.000 claims description 30
- 150000004767 nitrides Chemical class 0.000 claims description 25
- 229910052751 metal Inorganic materials 0.000 claims description 23
- 239000002184 metal Substances 0.000 claims description 23
- 239000000203 mixture Substances 0.000 claims description 10
- 150000002739 metals Chemical class 0.000 claims description 9
- 229910010271 silicon carbide Inorganic materials 0.000 claims description 4
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims description 4
- 229910052580 B4C Inorganic materials 0.000 claims description 3
- 229910052581 Si3N4 Inorganic materials 0.000 claims description 3
- HQVNEWCFYHHQES-UHFFFAOYSA-N silicon nitride Chemical compound N12[Si]34N5[Si]62N3[Si]51N64 HQVNEWCFYHHQES-UHFFFAOYSA-N 0.000 claims description 3
- INAHAJYZKVIDIZ-UHFFFAOYSA-N boron carbide Chemical compound B12B3B4C32B41 INAHAJYZKVIDIZ-UHFFFAOYSA-N 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims description 2
- 150000001247 metal acetylides Chemical class 0.000 claims description 2
- 230000000737 periodic effect Effects 0.000 claims description 2
- 229910052582 BN Inorganic materials 0.000 claims 1
- PZNSFCLAULLKQX-UHFFFAOYSA-N Boron nitride Chemical compound N#B PZNSFCLAULLKQX-UHFFFAOYSA-N 0.000 claims 1
- 239000002245 particle Substances 0.000 description 32
- 239000000843 powder Substances 0.000 description 28
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 26
- 229910052799 carbon Inorganic materials 0.000 description 25
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 18
- 229910052757 nitrogen Inorganic materials 0.000 description 9
- 238000002844 melting Methods 0.000 description 8
- 230000008018 melting Effects 0.000 description 8
- 239000007769 metal material Substances 0.000 description 8
- 230000003647 oxidation Effects 0.000 description 8
- 238000007254 oxidation reaction Methods 0.000 description 8
- 239000002994 raw material Substances 0.000 description 7
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 4
- 238000005245 sintering Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 239000003610 charcoal Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 239000011812 mixed powder Substances 0.000 description 3
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 3
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 2
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910001018 Cast iron Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 239000010730 cutting oil Substances 0.000 description 2
- -1 iron group metals Chemical class 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 239000010949 copper Substances 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005324 grain boundary diffusion Methods 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 229910021404 metallic carbon Inorganic materials 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 229910052755 nonmetal Inorganic materials 0.000 description 1
- 239000003921 oil Substances 0.000 description 1
- 239000004033 plastic Substances 0.000 description 1
- 229920003023 plastic Polymers 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000005060 rubber Substances 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000010936 titanium Substances 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J3/00—Processes of utilising sub-atmospheric or super-atmospheric pressure to effect chemical or physical change of matter; Apparatus therefor
- B01J3/06—Processes using ultra-high pressure, e.g. for the formation of diamonds; Apparatus therefor, e.g. moulds or dies
- B01J3/062—Processes using ultra-high pressure, e.g. for the formation of diamonds; Apparatus therefor, e.g. moulds or dies characterised by the composition of the materials to be processed
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J2203/00—Processes utilising sub- or super atmospheric pressure
- B01J2203/06—High pressure synthesis
- B01J2203/0605—Composition of the material to be processed
- B01J2203/062—Diamond
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J2203/00—Processes utilising sub- or super atmospheric pressure
- B01J2203/06—High pressure synthesis
- B01J2203/0605—Composition of the material to be processed
- B01J2203/0645—Boronitrides
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J2203/00—Processes utilising sub- or super atmospheric pressure
- B01J2203/06—High pressure synthesis
- B01J2203/065—Composition of the material produced
- B01J2203/0655—Diamond
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
- B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
- B01J2203/00—Processes utilising sub- or super atmospheric pressure
- B01J2203/06—High pressure synthesis
- B01J2203/065—Composition of the material produced
- B01J2203/066—Boronitrides
Landscapes
- Chemical & Material Sciences (AREA)
- Organic Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Ceramic Products (AREA)
Description
この発明は、すぐれた靭性および耐熱耐摩耗性
を有し、特に切削工具用材料として使用するのに
適した超高圧焼結材料に関するものである。
一般に、鋳鉄などの鉄系金属材料や、アルミニ
ウム、アルミニウム合金、銅、および銅合金など
の非鉄金属材料、さらにプラスチツク、ゴム、黒
鉛、セラミツクなどの非金属材料などの切削に使
用される切削工具には、高硬度、すぐれた耐摩耗
性、靭性、および熱的化学的安定性などの特性を
備えることが要求されている。
近年、かかる要求を満足すべく、主成分がダイ
ヤモンドからなる超高圧焼結材料が提案され、前
記超高圧焼結材料は常温は勿論のこと、比較的高
温においても高硬度を有し、すぐれた耐摩耗性を
示すことから、衝撃の加わるような苛酷な条件下
での仕上げ切削工具用材料として使用されてい
る。
確かに、上記超高圧焼結材料製切削工具によれ
ば、上記鉄系金属材料や非鉄金属材料の切削に際
して、高速切削が可能となるために、構成刃先が
つきにくく、すぐれた仕上げ面が得られるという
利点がもたらされる。
このように上記従来超高圧焼結材料は、主成分
が著しく高い硬さを有するダイヤモンドで構成さ
れているために、上記鉄系金属材料や非鉄金属材
料、および非金属材料の切削に切削工具として使
用した場合に、すぐれた耐摩耗性を示すものの、
十分な靭性を備えたものではないため、この靭性
不足が原因で切削時にチツピング摩耗を起し易
く、この結果本来具備しているすぐれた耐摩耗性
を十分発揮することができず、また十分な高温耐
酸化性（耐熱性）を備えていないために、温度上
昇を伴なう切削には使用することができないのが
現状である。
本発明者等は、上述のような観点から、靭性、
高温耐酸化性（耐熱性）、および耐摩耗性を兼ね
備えた切削工具用材料を得べく、ダイヤモンドに
着目して研究を行なつた結果、ダイヤモンド粉末
に、立方晶窒化ほう素（以下CBNで示す）粉末
と、周期律表の4a，5a、および6a族金属の炭化
物、同4aおよび5a族金属の窒化物および炭窒化
物、並びに同4a族金属のほう化物のうちの１種ま
たは２種以上（以下これらを総称して金属の炭・
窒・ほう化物という）からなる粉末と、さらに炭
化ほう素（以下B4Cで示す）、炭化けい素（以下
SiCで示す）、および窒化けい素（以下Si3N4で示
す）のうちの１種または２種以上（以下これらを
総称して炭・窒化物という）からなる粉末とを配
合したものを原料粉末として使用し、超高圧焼結
を施すと、ダイヤモンド粒子同志、CBN粒子同
志、金属の炭・窒・ほう化物粒子同志、および
炭・窒化物粒子同志の相互接触がなく、ダイヤモ
ンド粒子、CBN粒子、金属の炭・窒・ほう化物
粒子、および炭・窒化物粒子が相互に隣接し合
い、しかもその粒界では前記各粒子を構成する成
分の拡散が生じて強固な粒子間結合が形成されて
いる緻密な組織の焼結材料が得られ、この結果得
られた超高圧焼結材料は、ダイヤモンド粒子によ
つてもたらされるすぐれた耐摩耗性と、CBN粒
子、金属の炭・窒・ほう化物粒子、および炭・窒
化物粒子によつてもたらされるすぐれた靭性およ
び高温耐酸化性（耐熱性）とを兼ね備えるという
知見を得たのである。
したがつて、この発明は、上記知見にもとづい
てなされたもので、容量％で、
ダイヤモンド：20〜80％、
CBN：10〜70％、
金属の炭・窒・ほう化物：１〜30％、
炭・窒化物および不可避不純物：１〜30％、
からなる組成を有し、かつすぐれた靭性、耐熱
性、および耐摩耗性を有する切削工具用超高圧焼
結材料に特徴を有するものである。
ついで、この発明の超高圧焼結材料において、
成分組成範囲を上述の通りに限定した理由を説明
する。
(a) ダイヤモンド
ダイヤモンド自体は、周知のようにモース硬
さ：10、ヌープ硬さ：8000Kg／mm2（荷重100
ｇ）を有し、現存する物質中、最も高い硬さを
有する物質であるが、その含有量が20容量％未
満では、所望の耐摩耗性を確保することができ
ず、一方80容量％を越えて含有させると、ダイ
ヤモンド粒子相互間の接触度合が大きくなり、
特に靭性に富んだ金属の炭・窒・ほう化物粒子
と、特に高温耐酸化性にすぐれたCBN粒子、
および炭・窒化物粒子と、ダイヤモンド粒子と
の強固な粒子間結合が不十分となり、この結果
靭性低下をきたして切削時にチツピング摩耗が
生じやすくなることから、その含有量を20〜80
容量％と定めた。望ましくは40〜60容量％の含
有がよい。
また、この発明の超高圧焼結材料の製造に際
して、原料粉末として使用されるダイヤモンド
粉末は、すぐれた焼結性を確保する目的で、平
均粒径：50μｍ以下、一般には同10μｍ以下の
粉末粒径をもつものを使用するのが好ましく、
さらに市販のメタルコートのダイヤモンド粉末
を原料粉末として使用してもよい。
(b) CBN
CBNは、温度1200℃以上、圧力40Kb以上、
望ましくは温度1800℃以上、圧力60Kb以上の
条件で合成されるもので、ダイヤモンドに次ぐ
硬さ、すなわちビツカース硬さで6000〜7000
Kg／mm2を有し、かつダイヤモンドより高温まで
安定した性質をもつと共に、鉄族金属に対して
反応しにくい性質をもつ成分であるが、その含
有量が10容量％未満では、所望の高温耐酸化性
および鉄族金属に対する耐反応性を確保するこ
とができず、一方70容量％を越えて含有させる
と、相対的にダイヤモンドの含有量が少なくな
り過ぎて、ダイヤモンドのもつ高硬度を焼結材
料に十分反映させることができず、この結果耐
摩耗性の低下をもたらすようになることから、
その含有量を10〜70容量％に定めた。なお、望
ましくは30〜60容量％の含有がよい。
(c) 金属の炭・窒・ほう化物
例えば、炭化チタン（以下TiCで示す）は融
点：3147℃、微少硬さ：3000Kg／mm2（荷重100
ｇ）、窒化チタン（以下TiNで示す）は融点：
3205℃、微少硬さ：2000Kg／mm2、ほう化チタン
（以下TiB2で示す）は融点2980℃、微少硬さ：
3400Kg／mm2をそれぞれ有するように、金属の
炭・窒・ほう化物はいずれも高融点高融度を有
すると共に、ダイヤモンドに比して高温におけ
る耐酸化性にすぐれた物質であり、しかも金属
の炭・窒・ほう化物には、上述のように焼結時
にダイヤモンド粒子、CBN粒子、および炭・
窒化物粒子の間で粒界拡散を生じさせて強固な
粒子間結合を形成する作用があるほか、それ自
体が焼結性にすぐれたものであるため、ダイヤ
モンド粒子間をCBN粒子および炭・窒化物粒
子と共存した状態で埋めた緻密な組織を形成
し、靭性に寄与する作用があるが、その含有量
が１％未満では前記作用に所望の効果を確保す
ることができず、一方30容量％を越えて含有さ
せると、相対的にダイヤモンドの含有量が少な
くなつて、ダイヤモンドのもつ高硬度を焼結材
料に十分反映することができず、この結果耐摩
耗性の低下をきたすようになることから、その
含有量を１〜30容量％と定めた。
また、この発明の超高圧焼結材料の製造に際
して、原料粉末として使用される金属の炭・
窒・ほう化物粉末は微粉のものが好ましく、平
均粒径：10μｍ以下の微細な粉末を使用するの
が望ましい。
(d) 炭・窒化物
例えば、SiCは融点：2827℃、微少ヌープ硬
さ：3000Kg／mm2（荷重100ｇ）を有するよう
に、これら炭・窒化物はいずれも高融点高硬度
を有すると共に、ダイヤモンドに比して高温に
おける耐酸化性にすぐれた物質であり、しかも
炭・窒化物には、焼結時に、上述のようにダイ
ヤモンド粒子、CBN粒子、および金属の炭・
窒・ほう化粒子の相互粒界での成分拡散に寄与
して強固な粒子間結合を形成せしめる作用があ
るほか、それ自体が焼結性にすぐれたものであ
るため、ダイヤモンド粒子間をCBN粒子、お
よび金属の炭・窒・ほう化物粒子と共存した状
態で埋めた緻密な組織を形成して靭性向上に寄
与する作用があるが、その含有量が１容量％未
満では、前記作用に所望の効果が得られず、一
方30容量％を越えて含有させると、相対的にダ
イヤモンドの含有量が少なくなつて、ダイヤモ
ンドのもつ高硬度を焼結材料に十分反映するこ
とができず、この結果耐摩耗性低下をきたすよ
うになることから、その含有量を１〜30容量％
と定めた。
なお、この発明の超高圧焼結材料の製造に際
して、原料粉末として使用される炭・窒化物粉
末は、金属の炭・窒・ほう化物粉末と同様に、
望ましくは平均粒径：10μｍ以下の微細粉末の
使用がよい。
さらに、この発明の超高圧焼結材料は、通常
の粉末治金法により、公知の超高圧超高温発生
装置を使用して製造することができる。
すなわち、原料粉末としてのダイヤモンド粉
末、CBN粉末、金属の炭・窒・ほう化物粉
末、および炭・窒化物粉末を所定割合に配合
し、この配合粉末を鉄製ボールミルなどの混合
機において長時間混合して均質な混合粉末と
し、ついでこの混合粉末を、例えば特公昭36―
23463号公報に記載されるような超高圧高温発
生装置における鋼製あるいは高融点金属製の容
器内に封入し、圧力および温度を上げ、最高圧
力：54〜70Kb、最高温度：1400〜1800℃の範
囲内の圧力および温度に数分〜数10分保持した
後、冷却し、最終的に圧力を解放することから
なる基本的工程によつて製造することができ
る。
つぎに、この発明の超高圧焼結材料を実施例に
より説明する。
原料粉末として、それぞれ市販の平均粒径：３
μｍを有するダイヤモンド粉末、同６μｍの
CBN粉末、いずれも0.2〜２μｍの範囲内の平均
粒径を有する各種の金属の炭・窒・ほう化物粉
末、同３μｍのSiC粉末、同４μｍのB4C粉末、
および同２μｍのSi3N4粉末を用意し、これら原
料粉末をそれぞれ第１表に示される配合組成に配
合し、これに溶媒としてアセトンを加え、炭化タ
ングステン基超硬合金製のボールミル中で４時間
混合し、乾燥した後、直径：10mm×10mmの寸法を
もつたステンレス鋼（JIS・SUS304）製の管内に
詰め、真空引きしながらJIS・P20の炭化タング
ステン基超硬合金製の蓋を前記管の両側端部に溶
接して密封し、ついで、これを公知の超高圧高温
発生装置に装着し、最高付加圧力：60Kb、最高
加熱温度：1450℃の条件で10分間保持して焼結し
た後、冷却し、圧力解放を行なうことによつて実
質的に配合組成と同一の成分組成をもつた本発明
超高圧焼結材料１〜18、および比較超高圧焼結材
料１〜８をそれぞれ製造した。
この結果得られた本発明超高圧焼結材料１〜18
は、いずれもダイヤモンド、CBN、金属の炭・
窒・ほう化物、および炭・窒化物が均一に分散し
た緻密な組織をもつものであつた。
なお、比較超高圧焼結材料１〜８は、いずれも
構成成分のうちの少なくともいずれかの成分含有
量（第１表に※印を付したもの）がこの発明の範
囲から外れた組成をもつものである。
つぎに、上記の本発明超高圧焼結材料１〜18、
および比較超高圧焼結材料１〜８、並びに第１表
に示される組成をもつた従来公知の主成分がダイ
ヤモンドからなる市販の超高圧焼結材料から、切
断および研磨により切削用切刃を切出し、この切
刃を炭化タングステン基超硬合金製チツプに銀ろ
うを用いてろう付けした状態で、
被削材：FC20、
切削速度：400m／min、
切込み：0.35mm、
切削油：水溶性油使用、
の条件での鋳鉄の仕上げ面加工切削試験、並びに
被削材：Al―Si合金（Si：８重量％含有）、
切削速度：500m／min、
送り：0.08mm／rev.、
切込み：0.5mm、
切削油：なし、
の条件でのAl合金の仕上げ面加工切削試験を行
ない、いずれの切削試験でも切刃の逃げ面摩耗幅
が0.2mmに達するまでの切削時間を測定した。こ
れらの測定結果を第１表に示した。
第１表に示される結果から、本発明超高圧焼結
材料１〜18は、いずれも市販の超高圧焼結材料に
比して、著しくすぐれた靭性および耐熱性を有
The present invention relates to an ultra-high pressure sintered material that has excellent toughness and heat and wear resistance, and is particularly suitable for use as a material for cutting tools. Generally used for cutting tools used to cut ferrous metal materials such as cast iron, non-ferrous metal materials such as aluminum, aluminum alloys, copper, and copper alloys, and non-metallic materials such as plastics, rubber, graphite, and ceramics. are required to have properties such as high hardness, excellent wear resistance, toughness, and thermal and chemical stability. In recent years, in order to satisfy such demands, ultra-high pressure sintered materials whose main component is diamond have been proposed, and the ultra-high pressure sintered materials have high hardness not only at room temperature but also at relatively high temperatures, and have excellent properties. Because it exhibits wear resistance, it is used as a material for finishing cutting tools under harsh conditions such as impact. It is true that the above-mentioned cutting tool made of ultra-high pressure sintered material enables high-speed cutting when cutting the above-mentioned ferrous metal materials and non-ferrous metal materials, making it difficult for built-up edges to stick and providing an excellent finished surface. This provides the advantage of being able to In this way, the conventional ultra-high pressure sintered materials mentioned above are mainly composed of diamond which has extremely high hardness, so they can be used as cutting tools for cutting the above-mentioned ferrous metal materials, non-ferrous metal materials, and non-metal materials. Although it shows excellent wear resistance when used,
Because it does not have sufficient toughness, chipping wear is likely to occur during cutting due to this lack of toughness, and as a result, the excellent wear resistance that it originally has cannot be fully demonstrated, and the Currently, it cannot be used for cutting that involves a rise in temperature because it does not have high-temperature oxidation resistance (heat resistance). From the above-mentioned viewpoint, the present inventors have determined that toughness,
In order to obtain a material for cutting tools that has both high-temperature oxidation resistance (heat resistance) and wear resistance, we conducted research focusing on diamond. ) Powder and one or more of carbides of metals from groups 4a, 5a, and 6a of the periodic table, nitrides and carbonitrides of metals from groups 4a and 5a, and borides of metals from group 4a. (Hereinafter, these will be collectively referred to as metallic charcoal and
Powder consisting of nitrogen/boride), boron carbide (hereinafter referred to as B 4 C), and silicon carbide (hereinafter referred to as B4C).
The raw material is a mixture of silicon nitride (hereinafter referred to as Si 3 N 4 ) and powder consisting of one or more types of silicon nitride (hereinafter referred to as Si 3 N 4) (hereinafter collectively referred to as carbon/nitride). When used as a powder and subjected to ultra-high pressure sintering, there is no mutual contact between diamond particles, CBN particles, metal carbon/nitrogen/boride particles, and carbon/nitride particles, and diamond particles and CBN particles , metal carbon/nitride/boride particles and carbon/nitride particles are adjacent to each other, and the components constituting each particle are diffused at the grain boundaries, forming strong interparticle bonds. The resulting ultra-high pressure sintered material has excellent wear resistance brought about by diamond particles, CBN particles, and metal carbon/nitrogen/boride particles. , and the excellent toughness and high-temperature oxidation resistance (heat resistance) provided by carbon/nitride particles. Therefore, this invention was made based on the above knowledge, and in volume %, diamond: 20 to 80%, CBN: 10 to 70%, metal carbon/nitrogen/boride: 1 to 30%, The ultra-high pressure sintered material for cutting tools has a composition consisting of carbon/nitrides and unavoidable impurities: 1 to 30%, and has excellent toughness, heat resistance, and wear resistance. Next, in the ultra-high pressure sintered material of this invention,
The reason why the component composition range was limited as described above will be explained. (a) Diamond Diamond itself has a Mohs hardness of 10 and a Knoop hardness of 8000 kg/mm 2 (load of 100 kg).
g) and has the highest hardness among existing substances, but if the content is less than 20% by volume, the desired wear resistance cannot be secured; If the content exceeds the amount, the degree of contact between diamond particles increases,
Carbon/nitrogen/boride particles, which are metals with particularly high toughness, and CBN particles, which have particularly excellent high-temperature oxidation resistance,
The strong interparticle bond between carbon/nitride particles and diamond particles is insufficient, resulting in a decrease in toughness and easy chipping wear during cutting.
It was determined as capacity%. The content is preferably 40 to 60% by volume. In addition, in the production of the ultra-high pressure sintered material of this invention, the diamond powder used as the raw material powder has an average particle size of 50 μm or less, generally 10 μm or less, in order to ensure excellent sinterability. It is preferable to use one with a diameter,
Furthermore, commercially available metal-coated diamond powder may be used as the raw material powder. (b) CBN CBN has a temperature of 1200℃ or more, a pressure of 40Kb or more,
It is preferably synthesized at a temperature of 1,800℃ or higher and a pressure of 60Kb or higher, and has a hardness second only to diamond, i.e., 6,000 to 7,000 on the Vickers hardness.
Kg/mm 2 and has properties that are more stable at higher temperatures than diamond and less reactive with iron group metals. It is not possible to ensure oxidation resistance and reaction resistance to iron group metals, and on the other hand, if the content exceeds 70% by volume, the diamond content becomes relatively too small, and the high hardness of diamond is quenched. This is because the wear resistance cannot be sufficiently reflected in the bonding material, resulting in a decrease in wear resistance.
Its content was set at 10 to 70% by volume. Note that the content is preferably 30 to 60% by volume. (c) Metallic carbon, nitride, and borides For example, titanium carbide (hereinafter referred to as TiC) has a melting point of 3147℃ and a microhardness of 3000Kg/mm 2 (load of 100
g), Titanium nitride (hereinafter referred to as TiN) has a melting point:
3205℃, microhardness: 2000Kg/mm 2 , titanium boride (hereinafter referred to as TiB 2 ) has a melting point of 2980℃, microhardness:
3400Kg/ mm2 , the metals carbon, nitride, and borides all have high melting points and high melting points, and are substances with excellent oxidation resistance at high temperatures compared to diamond. As mentioned above, diamond particles, CBN particles, and carbon/borides are added to carbon/nitrogen/borides during sintering.
In addition to causing grain boundary diffusion between nitride particles and forming strong interparticle bonds, nitride itself has excellent sintering properties, so CBN particles and carbon/nitride It has the effect of forming a dense structure in coexistence with particles and contributing to toughness, but if its content is less than 1%, the desired effect cannot be achieved; If the content exceeds %, the diamond content becomes relatively low, and the high hardness of diamond cannot be fully reflected in the sintered material, resulting in a decrease in wear resistance. Therefore, its content was determined to be 1 to 30% by volume. In addition, when manufacturing the ultra-high pressure sintered material of this invention, metal charcoal and
The nitrogen/boride powder is preferably a fine powder, and it is desirable to use a fine powder with an average particle size of 10 μm or less. (d) Carbon/Nitride For example, SiC has a melting point of 2827°C and a micro Knoop hardness of 3000Kg/mm 2 (load 100g). All of these carbons and nitrides have a high melting point and high hardness. It is a substance that has better oxidation resistance at high temperatures than diamond, and carbon and nitrides also contain diamond particles, CBN particles, and metal carbon and nitrides during sintering, as described above.
In addition to contributing to component diffusion at mutual grain boundaries between nitride and boron grains and forming strong interparticle bonds, the CBN particles themselves have excellent sinterability. , and metal carbon/nitrogen/boride particles form a dense structure that contributes to improving toughness, but if the content is less than 1% by volume, the desired effect may not be achieved. On the other hand, if the content exceeds 30% by volume, the diamond content becomes relatively small, and the high hardness of diamond cannot be fully reflected in the sintered material, resulting in poor durability. The content should be reduced to 1 to 30% by volume as it will cause a decrease in abrasion properties.
It was determined that In addition, in the production of the ultra-high pressure sintered material of this invention, the carbon/nitride powder used as the raw material powder is similar to the metal carbon/nitride/boride powder.
It is preferable to use fine powder with an average particle size of 10 μm or less. Further, the ultra-high pressure sintered material of the present invention can be manufactured by a conventional powder metallurgy method using a known ultra-high pressure and ultra-high temperature generator. That is, raw material powders such as diamond powder, CBN powder, metal carbon/nitride/boride powder, and carbon/nitride powder are mixed in a predetermined ratio, and this mixed powder is mixed for a long time in a mixer such as an iron ball mill. Then, this mixed powder is made into a homogeneous mixed powder, for example, by
It is sealed in a container made of steel or high melting point metal in an ultra-high pressure and high temperature generator as described in Publication No. 23463, and the pressure and temperature are raised to achieve a maximum pressure of 54 to 70 Kb and a maximum temperature of 1400 to 1800°C. It can be produced by a basic process consisting of holding at a pressure and temperature range for a few minutes to several tens of minutes, then cooling and finally releasing the pressure. Next, the ultra-high pressure sintered material of the present invention will be explained using examples. As raw material powder, each commercially available average particle size: 3
Diamond powder with 6 μm
CBN powder, carbon/nitrogen/boride powder of various metals each having an average particle size within the range of 0.2 to 2 μm, SiC powder of 3 μm, B 4 C powder of 4 μm,
and Si 3 N 4 powder with a diameter of 2 μm were prepared, these raw material powders were blended into the composition shown in Table 1, acetone was added as a solvent, and the mixture was heated in a ball mill made of tungsten carbide-based cemented carbide. After mixing for a while and drying, it is packed into a stainless steel (JIS/SUS304) tube with dimensions of 10 mm x 10 mm in diameter, and while being evacuated, a JIS/P20 tungsten carbide-based cemented carbide lid is attached. Both ends of the tube were welded and sealed, and then this was attached to a known ultra-high pressure and high temperature generator, and sintered by holding it for 10 minutes at a maximum applied pressure of 60 Kb and a maximum heating temperature of 1450°C. Then, by cooling and releasing the pressure, ultra-high pressure sintered materials 1 to 18 of the present invention and comparative ultra-high pressure sintered materials 1 to 8 having substantially the same composition as the blended composition were produced, respectively. did. The resulting ultra-high pressure sintered materials 1 to 18 of the present invention
are diamond, CBN, metal charcoal,
It had a dense structure in which nitride/boride and carbon/nitride were uniformly dispersed. Comparative ultra-high pressure sintered materials 1 to 8 all have compositions in which the content of at least one of the constituent components (those marked with * in Table 1) is outside the scope of the present invention. It is something. Next, the above-mentioned ultra-high pressure sintered materials 1 to 18 of the present invention,
Cutting blades were cut by cutting and polishing from Comparative Ultra-High Pressure Sintered Materials 1 to 8 and conventionally known commercially available ultra-high pressure sintered materials consisting of diamond as the main component and having the compositions shown in Table 1. , this cutting edge is brazed to a tungsten carbide-based cemented carbide chip using silver solder, work material: FC20, cutting speed: 400 m/min, depth of cut: 0.35 mm, cutting oil: water-soluble oil used. Cutting test for finished surface machining of cast iron under the conditions of , Work material: Al-Si alloy (Si: 8% by weight), Cutting speed: 500 m/min, Feed: 0.08 mm/rev., Depth of cut: 0.5 mm , Cutting oil: None, Al alloy finishing cutting tests were conducted under the following conditions, and in each cutting test, the cutting time until the flank wear width of the cutting edge reached 0.2 mm was measured. The results of these measurements are shown in Table 1. From the results shown in Table 1, the ultra-high pressure sintered materials 1 to 18 of the present invention all have significantly superior toughness and heat resistance compared to commercially available ultra-high pressure sintered materials.
【表】【table】
【表】
し、かつこれと同等のすぐれた耐摩耗性を有する
ので、きわめて長い切削時間を示すのに対して、
市販の超高圧焼結材料は、靭性および耐熱性不足
が原因で比較的短かい切削時間しか示さないこと
が明らかである。
また、比較超高圧焼結材料１〜８に見られるよ
うに、構成成分のうちの少なくともいずれかの成
分含有量でもこの発明の範囲から外れると、靭
性、耐熱性、および耐摩耗性のうちの少なくとも
いずれかの性質が劣つたものになるので、所望の
切削性能を示さず、比較的短時間の切削時間しか
示さないものである。
上述のように、この発明の超高圧焼結材料は、
すぐれた靭性、耐熱性（高温耐酸化性）、よび耐
摩耗性を兼ね備えているので、特に切削工具用材
料として使用した場合にすぐれた切削性能を発揮
するのである。[Table] However, since it has the same excellent wear resistance as this, it shows an extremely long cutting time.
It is evident that commercially available ultra-high pressure sintered materials exhibit relatively short cutting times due to lack of toughness and heat resistance. Furthermore, as seen in Comparative Ultra-High Pressure Sintered Materials 1 to 8, if the content of at least one of the constituent components falls outside the scope of the present invention, the toughness, heat resistance, and wear resistance may deteriorate. Since at least one of the properties is inferior, it does not exhibit the desired cutting performance and exhibits only a relatively short cutting time. As mentioned above, the ultra-high pressure sintered material of this invention is
Because it has excellent toughness, heat resistance (high temperature oxidation resistance), and wear resistance, it exhibits excellent cutting performance especially when used as a material for cutting tools.
Claims (1)
4aおよび5a族金属の窒化物および炭窒化物、並び
に同4a族金属のほう化物のうちの１種または２種
以上：１〜30％、 炭化ほう素、炭化けい素、および窒化けい素の
うちの１種または２種以上および不可避不純物：
１〜30％、 からなる組成（以上容量％）を有することを特徴
とする靭性および耐熱耐摩耗性のすぐれた切削工
具用超高圧焼結材料。[Claims] 1. Diamond: 20-80%, cubic boron nitride: 10-70%, carbides of metals of groups 4a, 5a, and 6a of the periodic table,
One or more of nitrides and carbonitrides of group 4a and 5a metals, and borides of group 4a metals: 1 to 30%, among boron carbide, silicon carbide, and silicon nitride One or more of the following and unavoidable impurities:
An ultra-high pressure sintered material for cutting tools having excellent toughness and heat and wear resistance, characterized by having a composition (volume %) consisting of 1 to 30%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15148378A JPS5580775A (en) | 1978-12-09 | 1978-12-09 | Tanacious heattresisting antiabrasive super high pressure sintering material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15148378A JPS5580775A (en) | 1978-12-09 | 1978-12-09 | Tanacious heattresisting antiabrasive super high pressure sintering material |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5580775A JPS5580775A (en) | 1980-06-18 |
| JPS6143306B2 true JPS6143306B2 (en) | 1986-09-26 |
Family
ID=15519481
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15148378A Granted JPS5580775A (en) | 1978-12-09 | 1978-12-09 | Tanacious heattresisting antiabrasive super high pressure sintering material |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5580775A (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US4231195A (en) * | 1979-05-24 | 1980-11-04 | General Electric Company | Polycrystalline diamond body and process |
-
1978
- 1978-12-09 JP JP15148378A patent/JPS5580775A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS5580775A (en) | 1980-06-18 |
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