JPS61197469A - Manufacture of cubic boron nitride base sintering material for cutting tool - Google Patents
Manufacture of cubic boron nitride base sintering material for cutting toolInfo
- Publication number
- JPS61197469A JPS61197469A JP60037242A JP3724285A JPS61197469A JP S61197469 A JPS61197469 A JP S61197469A JP 60037242 A JP60037242 A JP 60037242A JP 3724285 A JP3724285 A JP 3724285A JP S61197469 A JPS61197469 A JP S61197469A
- Authority
- JP
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- Prior art keywords
- powder
- cbn
- cubic boron
- boron nitride
- cutting
- Prior art date
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Abstract
(57)【要約】本公報は電子出願前の出願データであるた
め要約のデータは記録されません。(57) [Summary] This bulletin contains application data before electronic filing, so abstract data is not recorded.
Description
【発明の詳細な説明】 〔産業上の利用分野〕 この発明は、すぐれた靭性と耐摩耗性を有し。[Detailed description of the invention] [Industrial application field] This invention has excellent toughness and wear resistance.
高硬度鋳鉄や、ダイス鋼および高速度鋼などの高硬度鋼
の切削、特にダイス鋼の７ライス切削などに切削工具と
して使用するのに適した立方晶窒化硼素（以下ＣＢＮで
示す）基焼結材料の製造方法に関するものである。Cubic boron nitride (hereinafter referred to as CBN)-based sintered material suitable for use as a cutting tool for cutting high-hardness cast iron, high-hardness steel such as die steel and high-speed steel, especially 7-rice cutting of die steel. This invention relates to a method for manufacturing materials.
従来、高硬度鋳鉄や上記高硬度鋼の切削、さらに切り込
みおよび送りの小さな切削に、鉄との反応がなく、ダイ
ヤモンドに次ぐ高硬度を有し、さらに高い熱伝導性を有
するｃＢＮを主成分として含有し、かつ、重量％で（以
下チは重量％を示す）、Ｔｉの炭化物、窒化物、および
炭窒化物（以下、それぞれＴｉＣ，ＴｉＮ、およびＴｉ
ＣＮで示し、これらを総称してＴｉの炭・窒化物という
）のうちの１種または２種以上：３〜３０％、
酸化アルミニウム（以下Ａｌ２Ｏ３で示す）および窒化
硅素（以下Ｓｉ３Ｎ、で示す）のうちの１種または２種
：４〜２５％。Conventionally, cBN, which does not react with iron, has a hardness second only to diamond, and has high thermal conductivity, has been used as a main ingredient for cutting high-hardness cast iron and the above-mentioned high-hardness steels, as well as for cutting with small depths of cut and feed. Ti carbides, nitrides, and carbonitrides (hereinafter TiC, TiN, and Ti
One or more of the following: 3 to 30% of aluminum oxide (hereinafter referred to as Al2O3) and silicon nitride (hereinafter referred to as Si3N); One or two of the following: 4-25%.
を含有し、残りが実質的に６０〜９３チのＣＢＮと不可
避不純物からなる組成を有するＣＢＮ基焼結材料が用い
られている。A CBN-based sintered material is used which has a composition containing CBN of 60-93% and the remainder substantially consisting of 60-93% CBN and unavoidable impurities.
このＣＢＮ基焼結材料は、原料粉末として、ＴｉＣ粉末
、 ＴｉＮ粉末、 ＴｉＣＮ粉末、Ａｌ２Ｏ，粉末、
Ｓｉ３Ｎ。This CBN-based sintered material contains TiC powder, TiN powder, TiCN powder, Al2O powder,
Si3N.
粉末、およびＣＢＮ粉末を用い、これら原料粉末を上記
の最終成分組成をもつように配合し１例えばボールミル
にて混合した後、０．５〜５０ｔｏｎ／ｃｎｌの圧力で
圧粉体にプレス成形し、ついで、この圧粉体をそのまま
、あるいは超高圧焼結の前処理として、１０〜１０
ｔｏｒｒの真空中または不活性ガス雰囲気中において８
００〜１２００℃の範囲内の所定温度で仮焼結して強度
を高めた状態で、かつ前記圧粉体または仮焼結体を単独
で、または炭化タングステン（ＷＣで示す）基超硬合金
やサーメット、さらにはＡｌ２Ｏ３基またはＳｉ、Ｎ、
基セラミックスの圧粉体または焼結体と重ね合わせて、
圧カニ１〜７０Ｐａ、温度＝１０００〜１８００℃、保
持時間二５〜１２０分の条件で製造されている。Using powder and CBN powder, these raw material powders are blended to have the above-mentioned final component composition, mixed in a ball mill, for example, and then press-molded into a green compact at a pressure of 0.5 to 50 ton/cnl. Next, this green compact is heated as it is or as a pretreatment for ultra-high pressure sintering for 10 to 10 minutes.
8 in a vacuum of torr or in an inert gas atmosphere.
In a state where the strength is increased by pre-sintering at a predetermined temperature within the range of 00 to 1200°C, the green compact or the pre-sintered compact is used alone or with tungsten carbide (indicated by WC) based cemented carbide or Cermet, further Al2O3 group or Si, N,
Layered with a compacted powder or sintered body of base ceramics,
It is manufactured under the following conditions: pressure crab: 1-70 Pa, temperature: 1000-1800° C., holding time: 25-120 minutes.
近年、切削加工の分野においては、鋳鉄切削の高速化や
、ダイス鋼や高速度鋼などの高硬度鋼の研削加工から切
削加工への切り換えがさけばれるようになシ、これに伴
い、上記のＣＢＮ基焼結材料を、これらの切削に用いる
試みもなされたが、このＣＢＮ基焼結材料は、靭性に劣
るものであるのに加えて、被剛材たる高硬度鋳鉄のチル
ド鋳鉄はショア硬さで約８０．また上記の高硬度鋼は熱
処理状態でロックウェル硬さくＣスケール）で５０以上
の高硬度を有する一方、切削速度の高速化、切シ込みの
増大、さらに送り速度の高速化にしたがって旋盤加工時
に刃先に対して加わる負荷がきわめて大きくなることか
ら、刃先の欠損や摩耗が著しく、実用に供し得ないのが
現状である。In recent years, in the field of cutting, the speed of cutting cast iron has increased, and the switch from grinding to cutting of high-hardness steels such as die steel and high-speed steel has been avoided. Attempts have been made to use CBN-based sintered materials for these types of cutting, but in addition to this CBN-based sintered material having inferior toughness, the high hardness chilled cast iron used as the material to be stiffened has shore hardness. Approximately 80. In addition, while the above-mentioned high-hardness steel has a high hardness of 50 or more on the Rockwell hardness scale (C scale) in the heat-treated state, it is difficult to use it during lathe processing due to faster cutting speeds, larger depths of cut, and faster feed rates. Since the load applied to the cutting edge becomes extremely large, the cutting edge is severely damaged and worn out, making it currently unusable.
そこで１本発明者等は、上述のような観点から。 Therefore, the inventors of the present invention, etc., from the above-mentioned viewpoint.
上記の従来切削工具用ＣＢＮ基焼結材料に着目し。Focusing on the above-mentioned conventional CBN-based sintered material for cutting tools.
これに靭性を付与して、鋳鉄の高速切削や、高硬度鋼の
切削加工に切削工具として使用することのできるＣＢＮ
基焼結材料を製造すべく研究を行なった結果。CBN can be used as a cutting tool for high-speed cutting of cast iron and cutting of high-hardness steel by adding toughness to it.
The result of research to produce base sintered materials.
（ａ） 従来方法におけるように、原料粉末として。(a) As a raw powder, as in conventional methods.
ＣＢＮ粉末、Ｔｉの炭・窒化物粉末、並びにＡ＋！２０
３粉末および／またはＳｉ３Ｎ、粉末を用い、これらの
混合粉末よシ成形した圧粉体を超高圧下で焼結した場合
、 Ｔｉの炭・窒化物粉末、ＡＸ２０３粉末、およびＳ
ｉ３Ｎ。CBN powder, Ti carbon/nitride powder, and A+! 20
3 powder and/or Si3N powder, and when a green compact formed from these mixed powders is sintered under ultra-high pressure, Ti carbon/nitride powder, AX203 powder, and S
i3N.
粉末は、 ＣＢＮ粉末に比して軟質なために塑性変形し
てＣＢＮ粒子の界面に廻シ込むものの１両者間に反応が
生じないので、界面強度ひいては靭性の向上は得られな
いこと。Since the powder is softer than CBN powder, it deforms plastically and penetrates into the interface of CBN particles, but since no reaction occurs between the two, no improvement in interface strength or toughness can be obtained.
（ｂ） これに対して、従来方法で用いられている原
料粉末に加えて、チタン・アルミニウム炭化物（以下Ｔ
ｉ□ＡｇＣで示す）粉末および／またはチタン・アルミ
ニウム炭窒化物（以下Ｔｉ□Ａ１ＣＮで示す）粉末を用
いると、これらの粉末は超高圧焼結時の１３００℃以上
の温度で徐々に分解再反応を起してＴｉＣあるいはＴｉ
ＣＮを生成し、この分解生成したＴｉＣあるいはＴｉＣ
ＮはＣＢＮ粒との界面に層状の反応領域を形成し、しか
もこの反応領域中にはＭの存在は認められず、Ａｌｌは
反応領域外のＴｉＣあるいはＴｉＣＮ内に均一に分布し
、かつＡＩＮの形成も認められないことから、充分な焼
結促進効果が得られるようになると共に、焼結材料特性
、特に靭性が著しく向上するようになること。(b) On the other hand, in addition to the raw material powder used in the conventional method, titanium aluminum carbide (hereinafter T
When using i□AgC) powder and/or titanium aluminum carbonitride (hereinafter referred to as Ti□A1CN) powder, these powders gradually decompose and re-react at temperatures of 1300°C or higher during ultra-high pressure sintering. TiC or Ti
CN is generated, and TiC or TiC produced by this decomposition
N forms a layered reaction region at the interface with the CBN grains, and the presence of M is not recognized in this reaction region, and All is uniformly distributed in TiC or TiCN outside the reaction region, and Since no formation is observed, a sufficient sintering promotion effect can be obtained, and the properties of the sintered material, especially toughness, can be significantly improved.
（Ｃ） 上記のＴｉ□ＡｌＣあるいはＴｉ□ＡｇＣＮ
粉末の分解によって生成した反応領域外のＴｉＣ、りる
いはＴｉＣＮは焼結材料中で均一な微細分散構造をとる
こと。(C) The above Ti□AlC or Ti□AgCN
TiC, lubrication, or TiCN generated by decomposition of the powder outside the reaction area should have a uniform finely dispersed structure in the sintered material.
（ｄ） 一方、上記ノＴｉ２ＡｌＩＣ粉末あるいはＴ
ｉ□ＡｇＣＮ粉末に代えて、原料粉末として１例えばＴ
ｌＡ１３などのＴｉ−Ａε金属間化合物粉末を用いると
、超高圧焼結時にＴｉ８ｇやＪＡＮを生成してしまい、
これが原因で充分な焼結促進効果が得られず、靭性のす
ぐれた焼結材料を得ることはできないこと。(d) On the other hand, the above Ti2AlIC powder or T
i□In place of AgCN powder, 1, for example T, is used as raw material powder.
If Ti-Aε intermetallic compound powder such as lA13 is used, Ti8g and JAN will be generated during ultra-high pressure sintering.
Due to this, a sufficient sintering promotion effect cannot be obtained and a sintered material with excellent toughness cannot be obtained.
以上（ａ）〜（ｄ）に示される知見を得たのである。The findings shown in (a) to (d) above were obtained.
この発明は、上記知見にもとづいてなされたものであっ
て、原料粉末として、 ＣＢＮ粉末、 Ｍ２Ｏ３粉末、
Ｓｉ３Ｎ、粉末、およびＴｉの炭・窒化物粉末、さ
らにＴｉ２ＡｊＩＣ粉末およびＴｉ２ＡｌｔＣ’Ｎ粉末
を用い、これら原料粉末を、
Ｔｉの炭・窒化物のうちの１種または２種以上：２〜１
５％。This invention was made based on the above knowledge, and raw material powders include CBN powder, M2O3 powder,
Using Si3N, powder, and Ti carbon/nitride powder, as well as Ti2AjIC powder and Ti2AltC'N powder, these raw material powders are mixed with one or more of Ti carbon/nitride: 2 to 1
5%.
Ｔ ｉ ２ Ｍ、 ＣおよびＴｉ□ＭＣＮのうちの１種
または２種：１〜２０％、
ｆｉＪｌ ２０３および５１３Ｎ４のうちの１種または
２種二４〜２５％。One or two of Ti2M, C and Ti□MCN: 1-20%, one or two of fiJl 203 and 513N4 24-25%.
ＣＢＮ 二 ６０〜９３％。CBN 2 60-93%.
からなる配合組成に配合し、上記のように５通常の条件
にて混合した後、圧粉体にプレス成形し。After mixing under normal conditions as described above, the mixture was press-molded into a green compact.
さらに通常の条件にて超高圧焼結することによって、従
来切削工具用ＣＢＮ基焼結材料と実質的に同じ成分組成
、すなわち。Further, by performing ultra-high pressure sintering under normal conditions, the composition is substantially the same as that of conventional CBN-based sintered materials for cutting tools.
Ｔｉの炭・窒化物のうちの１種または２種以上＝３〜３
０％。One or more of Ti carbon/nitride = 3 to 3
0%.
Ａｌ２Ｏ３およびＳｉ３Ｎ、のうちの１種または２種：
４〜２５％。One or two of Al2O3 and Si3N:
4-25%.
を含有し、残りが実質的に６０〜９３％のＣＢＮと不可
避不純物からなる組成をもった靭性および耐摩耗性にす
ぐれた切削工具用ＣＢＮ基焼結材料を製造する方法に特
徴を有するものである。The method is characterized by a method for producing a CBN-based sintered material for cutting tools with excellent toughness and wear resistance, with the remainder consisting essentially of 60 to 93% CBN and unavoidable impurities. be.
つぎに、この発明の方法における配合組成を上記の通り
に限定した理由を説明する。Next, the reason why the composition in the method of this invention is limited as described above will be explained.
（ａ） Ｔｉの炭・窒化物
これらの成分には、焼結材料に耐溶着性を付与する作用
があるが、その配合量が２チ未満では実質的にＴｉ２Ａ
ｇＣ４るいはＴｉ２ＡｇＣＮの分解によって生成するＴ
ｉＣあるいはＴｉＣＮと合わせても焼結材料中の含有量
が３％未満となってしまい、所望のすぐれた耐溶着性を
確保することができず、この結果切削加工時に刃先に溶
着が生じ易くなって刃先のチッピングや摩耗が促進され
るようになり、一方１５％を越えて配合すると、 Ｔｉ
２ＡＥＣあるいはＴｉ□ＡＡＣＮとの配合割合との関係
で焼結材料中の含有量が３０％を越えて高くなる場合が
生じ、このような場合には硬さの低下が著しく、所望の
耐摩耗性を確保することができなくなることから、その
配合量を２〜１５％と定めた。(a) Ti carbon/nitride These components have the effect of imparting adhesion resistance to the sintered material, but if the amount is less than 2 Ti, it will essentially become Ti2A.
T produced by decomposition of gC4 or Ti2AgCN
Even when combined with iC or TiCN, the content in the sintered material is less than 3%, making it impossible to secure the desired excellent welding resistance, and as a result, welding tends to occur on the cutting edge during cutting. On the other hand, if the Ti content exceeds 15%
Depending on the blending ratio of 2AEC or Ti□AACN, the content in the sintered material may exceed 30%, and in such cases, the hardness decreases significantly and the desired wear resistance cannot be achieved. Since it becomes impossible to ensure the above, the blending amount was determined to be 2 to 15%.
（ｂ） Ｔｉ□Ａ１．ＣおよびＴｉ□ＡｌＣＮこれら
の成分には、上記したように超高圧焼結時に分解反応を
起してＴｉＣあるいはＴｉＣＮを生成し、このＴＩＣあ
るいはＴｉＣＮはＣＢＮ粒子と他の配合粒子との間に廻
り込んで直接の接触を阻止すると共に、 ＣＢＮ粒子と
の界面に反応領域層を形成して焼結材料の靭性を著しく
向上させる作用があるが、その配合量が１％未満では所
望の靭性向上効果が得られず、一方２０％を越えて配合
すると。(b) Ti□A1. C and Ti□AlCN As mentioned above, these components undergo a decomposition reaction during ultra-high pressure sintering to produce TiC or TiCN, and this TIC or TiCN is distributed between CBN particles and other blended particles. It has the effect of blocking direct contact with the CBN particles and significantly improving the toughness of the sintered material by forming a reaction zone layer at the interface with the CBN particles, but if the amount is less than 1%, the desired toughness improvement effect is not achieved. On the other hand, if it is blended in excess of 20%.
焼結材料中のＴｉの炭・窒化物の含有量が３０チを越え
て高くなる場合が生じ、耐摩耗性の著しい劣化を招くよ
うになることから、その配合量を１〜２０％と定めた。The content of Ti carbon/nitride in the sintered material may exceed 30 Ti, which causes a significant deterioration of wear resistance, so the content is set at 1 to 20%. Ta.
（Ｃ）Ａ１２０３およびＳｉ３Ｎ。(C) A1203 and Si3N.
これらの成分には、焼結材料の耐摩耗性および耐溶着性
を向上させる作用があるが、その配合量が４１未満では
実質的に焼結材料中の含有量も４チ未満となってしまい
所望の耐摩耗性および耐溶着性を確保することができず
、一方２５％を越えて配合すると、焼結材料中の含有量
も２５％を越えて高くなってしまい、靭性低下をきたし
て刃先にチッピングが生じ易くなることから、その配合
量を４〜２５％と定めた。These components have the effect of improving the wear resistance and welding resistance of the sintered material, but if the amount of these components is less than 41, the content in the sintered material will essentially be less than 4. It is not possible to secure the desired wear resistance and welding resistance, and on the other hand, if the content exceeds 25%, the content in the sintered material will also be high, exceeding 25%, resulting in a decrease in toughness and damage to the cutting edge. Since chipping is likely to occur in this case, the blending amount was set at 4 to 25%.
（ｄ）ＣＢＮ
焼結材料のすぐれた耐摩耗性および耐欠損性はＣＢＮ成
分によってもたらされるが、その配合量が６０チ未満で
は、実質的に焼結材料中の含有量も６０％未満となって
しまい、特に所望の耐摩耗性を確保することが困難にな
り、一方９３チを越えて配合すると、同様に焼結材料中
の含有量も９３チを越えて高くなシ、特に耐欠損性に著
しい劣化現象が現われるようになることから、その配合
量を６０〜９３％と定めた。(d) CBN The excellent wear resistance and chipping resistance of the sintered material is brought about by the CBN component, but if the amount is less than 60%, the content in the sintered material will essentially be less than 60%. On the other hand, if more than 93 g is mixed, the content in the sintered material will also be high, especially if it exceeds 93 g. Since a significant deterioration phenomenon appears in the above, the blending amount was determined to be 60 to 93%.
なお、この発明の方法を実施するにあたって採用される
圧力および温度は、ＣＢＮの安定領域内の条件としても
よいが、必ずしもそれほどの超高圧、高温は必要でない
。その理由は、原料粉末としてＴｉ□ＵＣ粉末あるいは
Ｔｉ２ＡｌＩＣＮ粉末を用いると、前記のようにＣＢＮ
粒の界面にＭの存在（−ない反応領域が生成し、この反
応領域層には立方晶から六方晶への逆変態を抑制する作
用があり、この結果比較的低い圧力条件下でも所望の焼
結材料を製造することが可能となるからである。この現
象は原料粉末としてＴｉＡｌ３などの金属間化合物を用
いた場合には見られない現象である。Note that the pressure and temperature employed in implementing the method of the present invention may be within the stable region of CBN, but extremely high pressures and high temperatures are not necessarily required. The reason is that when Ti□UC powder or Ti2AlICN powder is used as the raw material powder, CBN
The presence of M (-) forms a reaction region at the grain interface, and this reaction region layer has the effect of suppressing the reverse transformation from cubic to hexagonal. As a result, the desired sintering can be achieved even under relatively low pressure conditions. This is because it becomes possible to produce a bonding material.This phenomenon is not observed when an intermetallic compound such as TiAl3 is used as the raw material powder.
つぎに、この発明の方法を実施例によシ具体的に説明す
る。Next, the method of the present invention will be specifically explained using examples.
原料粉末として、平均粒径：２μｍを有するＣＢＮ粉末
、いずれも同１μｍを有するＴｉＣ粉末。The raw material powders were CBN powder with an average particle size of 2 μm and TiC powder with an average particle size of 1 μm.
ＴｉＮ粉末、およびＴｉＣＮ （ＴｉＣ／ＴｉＮ−５０
１５０）粉末、同３μｍのＴｉ□／Ｖ、Ｃ粉末、同１μ
ｍのＴｉ２ＡＺＣＮ（Ｃ／Ｎ ＝ ６ ／４ ）粉末、
同０．５μｍのＡｌ２Ｏ３粉末、同４μｍのＳｉ３Ｎ、
粉末、並びに同１μｍのＴｉＡｌ３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、ボールミルにて１６時間混合した後、 １ ｔｏ
ｎ／ｃｒｉの圧力にて圧粉体にプレス成形し、ついでこ
の圧粉体を温度：９００℃に１時間保持して仮焼結した
後、ベルト型超高圧装置に装入し、４〜’７ ＧＰａの
範囲内の所定の圧力を付加した状態で、１３００〜１６
００℃の範囲内の所定温度に１０分間保持して超高圧焼
結し、冷却・除圧することによって本発明焼結材料１〜
１２および比較焼結材料１〜３をそれぞれ製造した。TiN powder, and TiCN (TiC/TiN-50
150) Powder, 3 μm Ti□/V, C powder, 1 μm
m of Ti2AZCN (C/N = 6/4) powder,
0.5 μm Al2O3 powder, 4 μm Si3N,
Powder and TiAl3 powder of the same 1 μm were prepared, and these raw material powders were blended into the composition shown in Table 1, and after mixing in a ball mill for 16 hours, 1 to
The compact was press-formed at a pressure of n/cri, then the compact was held at a temperature of 900°C for 1 hour for temporary sintering, and then charged into a belt-type ultra-high pressure device for 4~' 1300 to 16 with a predetermined pressure within the range of 7 GPa applied.
The sintered materials 1 to 1 of the present invention are prepared by holding at a predetermined temperature within the range of 00°C for 10 minutes, performing ultra-high pressure sintering, cooling and depressurizing.
No. 12 and Comparative Sintered Materials 1-3 were produced, respectively.
なお、比較焼結材料ｌ、２は従来方法にもとづいて製造
されたものでちゃ、比較焼結材料３は原料粉末としてＴ
ｉ２ＡＺＣあるいはＴｉ２ＡＬＣＮ粉末に代って従来公
知の金属間化合物であるＴｌＡ１３粉末を用いて製造し
たものである。In addition, comparative sintered materials 1 and 2 were manufactured based on the conventional method, and comparative sintered material 3 was manufactured using T as a raw material powder.
It was manufactured using TlA13 powder, which is a conventionally known intermetallic compound, instead of i2AZC or Ti2ALCN powder.
ついで、この結果得られた本発明焼結材料１〜１２およ
び比較焼結材料１〜３について、靭性を評価する目的で
破壊靭性値を測定し、また耐摩耗性を評価する目的でビ
ッカース硬さを測定し、さらにこれより研削・研摩仕上
げにより切削工具用切刃を作製し、
被削材：高速度鋼（ＳＫＤ ６１．ＨＲＣ：６０）。Next, for the resulting sintered materials 1 to 12 of the present invention and comparative sintered materials 1 to 3, fracture toughness values were measured for the purpose of evaluating toughness, and Vickers hardness was measured for the purpose of evaluating wear resistance. was measured, and a cutting edge for a cutting tool was made by grinding and polishing. Workpiece material: High speed steel (SKD 61.HRC: 60).
切削速度： ２００ ｍ １ｍｈ。Cutting speed: 200m 1mh.
゛切込み：０．５ｍｍ。゛Depth of cut: 0.5mm.
ｌ刃自りの送シ：０．１馴／刃。lBlade own feed: 0.1 familiarity/blade.
測定した。これらの測定結果を第１表に合せて示した。It was measured. These measurement results are also shown in Table 1.
第１表に示されるように１本発明焼結材料１〜１２は、
いずれもすぐれた靭性と耐摩耗性を有するので、著しく
長期に亘ってすぐれた切削性能を発揮するのに対して、
従来方法によって製造された比較焼結材料１．２および
原料粉末としてＴｉＡＡ３粉末を用いて製造された比較
焼結材料３は、いずれも靭性不足が原因で切削開始後、
短時間で切刃に欠けが発生し、使用寿命に至るものであ
った。As shown in Table 1, the sintered materials 1 to 12 of the present invention are:
Both have excellent toughness and wear resistance, so they exhibit excellent cutting performance over an extremely long period of time.
Comparative sintered material 1.2 manufactured by the conventional method and comparative sintered material 3 manufactured using TiAA3 powder as the raw material powder both had poor toughness after starting cutting due to insufficient toughness.
The cutting edge would chip in a short period of time, reaching the end of its service life.
上述のように、この発明の方法によれば、靭性および耐
摩耗性にすぐれ、鋳鉄の高速切削や、高硬度鋼の切削に
切削工具として用いることのできるＣＢＮ基焼結材料を
製造することができるのである。As described above, according to the method of the present invention, it is possible to produce a CBN-based sintered material that has excellent toughness and wear resistance and can be used as a cutting tool for high-speed cutting of cast iron and cutting of high-hardness steel. It can be done.
Claims (1)
たは２種以上：３〜３０％、 酸化アルミニウムおよび窒化硅素のうちの１種または２
種：４〜２５％、 を含有し、残りが実質的に６０〜９３％の立方晶窒化硼
素と不可避不純物からなる組成を有する立方晶窒化硼素
基焼結材料を製造するに際して、原料粉末として、 Ｔｉの炭化物粉末、窒化物粉末、および炭窒化物粉末の
うちの１種または２種以上：２〜１５％、チタン・アル
ミニウム炭化物粉末およびチタン・アルミニウム炭窒化
物粉末のうちの１種または２種：１〜２０％、 酸化アルミニウム粉末および窒化硅素粉末のうちの１種
または２種：４〜２５％、 立方晶窒化硼素粉末：６０〜９３％、 からなる配合組成（以上重量％）を有する混合粉末を用
いることを特徴とする靭性および耐摩耗性のすぐれた切
削工具用立方晶窒化硼素基焼結材料の製造方法。[Claims] One or more of Ti carbides, nitrides, and carbonitrides: 3 to 30%, one or two of aluminum oxide and silicon nitride
When producing a cubic boron nitride-based sintered material having a composition containing 4 to 25% of seeds, with the remainder substantially consisting of 60 to 93% of cubic boron nitride and unavoidable impurities, as a raw material powder, One or more of Ti carbide powder, nitride powder, and carbonitride powder: 2 to 15%, one or two of titanium/aluminum carbide powder and titanium/aluminum carbonitride powder : 1 to 20%; one or two of aluminum oxide powder and silicon nitride powder: 4 to 25%; cubic boron nitride powder: 60 to 93%; A method for producing a cubic boron nitride-based sintered material for cutting tools having excellent toughness and wear resistance, characterized by using powder.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60037242A JPS61197469A (en) | 1985-02-26 | 1985-02-26 | Manufacture of cubic boron nitride base sintering material for cutting tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP60037242A JPS61197469A (en) | 1985-02-26 | 1985-02-26 | Manufacture of cubic boron nitride base sintering material for cutting tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS61197469A true JPS61197469A (en) | 1986-09-01 |
| JPH0225871B2 JPH0225871B2 (en) | 1990-06-06 |
Family
ID=12492147
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP60037242A Granted JPS61197469A (en) | 1985-02-26 | 1985-02-26 | Manufacture of cubic boron nitride base sintering material for cutting tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS61197469A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001206773A (en) * | 2000-01-25 | 2001-07-31 | Natl Inst Of Advanced Industrial Science & Technology Meti | Cubic boron nitride-based sintered material and method of producing the same |
| WO2010119962A1 (en) * | 2009-04-17 | 2010-10-21 | 株式会社タンガロイ | Cubic boron nitride sintered compact and coated cubic boron nitride sintered compact |
| CN103820691A (en) * | 2014-02-27 | 2014-05-28 | 西安石油大学 | Preparation method for sintering FeAl/TiC composite material under normal pressure |
| JPWO2021010472A1 (en) * | 2019-07-18 | 2021-09-13 | 住友電気工業株式会社 | Cubic boron nitride sintered body and cutting tool |
-
1985
- 1985-02-26 JP JP60037242A patent/JPS61197469A/en active Granted
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001206773A (en) * | 2000-01-25 | 2001-07-31 | Natl Inst Of Advanced Industrial Science & Technology Meti | Cubic boron nitride-based sintered material and method of producing the same |
| US6562746B2 (en) | 2000-01-25 | 2003-05-13 | Aisin Seiki Kabushiki Kaisha | Cubic boron nitride-based sintered material and manufacture thereof |
| JP4560604B2 (en) * | 2000-01-25 | 2010-10-13 | 独立行政法人産業技術総合研究所 | Cubic boron nitride based sintered material and method for producing the same |
| WO2010119962A1 (en) * | 2009-04-17 | 2010-10-21 | 株式会社タンガロイ | Cubic boron nitride sintered compact and coated cubic boron nitride sintered compact |
| JP5660034B2 (en) * | 2009-04-17 | 2015-01-28 | 株式会社タンガロイ | Cubic boron nitride sintered body and coated cubic boron nitride sintered body |
| CN103820691A (en) * | 2014-02-27 | 2014-05-28 | 西安石油大学 | Preparation method for sintering FeAl/TiC composite material under normal pressure |
| CN103820691B (en) * | 2014-02-27 | 2015-11-11 | 西安石油大学 | A kind of normal pressure-sintered preparation method of FeAl/TiC matrix material |
| JPWO2021010472A1 (en) * | 2019-07-18 | 2021-09-13 | 住友電気工業株式会社 | Cubic boron nitride sintered body and cutting tool |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0225871B2 (en) | 1990-06-06 |
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