JP4244108B2 - CUTTING TOOL CUTTING PART OF Cubic Boron Nitride-Based Sintered Material with Excellent Chipping Resistance - Google Patents
CUTTING TOOL CUTTING PART OF Cubic Boron Nitride-Based Sintered Material with Excellent Chipping Resistance Download PDFInfo
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Description
【０００１】
【発明の属する技術分野】
この発明は、特に高硬度焼入れ鋼や鋳鉄などの表面仕上加工を断続切削条件で行なった場合にも、すぐれた耐チッピング性を発揮する立方晶窒化ほう素（以下、ｃ−ＢＮで示す）基焼結材料製切削工具切刃片の製造方法に関するものである。
【０００２】
【従来の技術】
従来、一般に切刃片としてｃ−ＢＮ基焼結材料を用いた切削工具としては、例えば特公平１−１６８９４号公報の実施例に記載されるように、ｃ−ＢＮ基焼結材料からなる切刃片、あるいはｃ−ＢＮ基焼結材料の切刃片とＷＣ基超硬合金の支持片からなる複合体を通常の超高圧焼結装置を用いて製造し、これを、ＷＣ基超硬合金からなる工具本体の切刃部に、質量％で、例えばＣｕ：３０％、Ｚｎ：２８％、Ｎｉ：２％を含有し、残りがＡｇと不可避不純物からなる組成を有するＡｇ合金のろう材を用いてろう付けしてなる切削工具が広く知られており、これがスローアウエイチップ（以下、単にチップと云う）やドリル、さらにエンドミルやリーマなどの切削工具として、高硬度焼入れ鋼や鋳鉄などの表面仕上加工に連続切削条件で用いられることも良く知られるところである。
また、上記の切削工具切刃片として、例えば特開昭５６−１５６３３８号公報に記載されるように、走査型電子顕微鏡による組織観察で、ｃ−ＢＮからなる硬質分散相と、炭化チタン、窒化チタン、および炭窒化チタン（以下、それぞれＴｉＣ、ＴｉＮ、およびＴｉＣＮ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Ｔｉ炭・窒化物という）からなる連続結合相で構成された組織を示し、かつ、
上記硬質分散相：５０〜７０面積％、
上記連続結合相および不可避不純物：残り、
からなる組成を有するｃ−ＢＮ基焼結材料で構成した切削工具切刃片が知られている。
【０００３】
【発明が解決しようとする課題】
一方、近年の切削加工は、切削加工装置の高性能化と相俟って多様化し、かつ切削加工の省力化および省エネ化、さらに低コスト化に対する要求も強く、これに伴なって、切削工具にもできるだけ切削加工条件に制約されない汎用性が求められる傾向にあるが、上記の従来ｃ−ＢＮ基焼結材料製切削工具切刃片においては、表面仕上加工を連続切削条件で行なうのに用いた場合には問題はないが、これを断続切削条件での表面仕上加工に用いると、硬質分散相と連続結合相間の密着性が十分でないために前記硬質分散相に剥離現象が発生するようになり、これが原因で切刃部にチッピング（微小欠け）が発生し、比較的短時間で使用寿命に至るのが現状である。
【０００４】
【課題を解決するための手段】
そこで、本発明者等は、上述のような観点から、上記の従来ｃ−ＢＮ基焼結材料製切削工具切刃片に着目し、これの耐チッピング性向上を図るべく研究を行なった結果、
（ａ）まず、原料粉末として、ｃ−ＢＮ粉末、Ｔｉ炭・窒化物粉末、Ｔｉ−Ａｌ合金粉末、望ましくはＴｉ−Ａｌ金属間化合物粉末、および炭化タングステン（以下、ＷＣで示す）粉末を用意し、これら原料粉末を所定の配合組成に配合し、混合した後、圧粉体にプレス成形し、ついでこの圧粉体に、真空雰囲気中、９００〜１３００℃の範囲内の所定温度に所定時間保持の条件で反応処理を施すと、前記圧粉体におけるｃ−ＢＮ粉末は熱的安定性にすぐれているので、前記焼結処理によって実質的に反応せず、そのままの状態で残るが、Ｔｉ−Ａｌ合金粉末とＷＣ粉末は反応し、これらは前記ｃ−ＢＮ粉末の表面部とも反応してＴｉ−Ａｌ−Ｗ系炭窒ほう化物を形成することから、きわめて硬質のｃ−ＢＮからなる硬質分散相がＴｉ−Ａｌ−Ｗ系炭窒ほう化物で強固に結合された組織を有する反応焼結材料が形成されるようになること。
【０００５】
（ｂ）上記（ａ）の反応焼結材料を粉砕して、粉砕後の個々の粉末をきわめて硬質のｃ−ＢＮの表面にＴｉ−Ａｌ−Ｗ系炭窒ほう化物が強固に結合してなる複合粉末とし、この複合粉末を２次原料粉末とし、これに別途用意したＴｉ炭・窒化物粉末を所定の割合に配合し、混合した後、所定の圧力で圧粉体にプレス成形し、この圧粉体を、真空雰囲気中、９００〜１３００℃の範囲内の所定温度に所定時間保持の条件で焼結して１次焼結材料とした状態で、通常の超高圧焼結装置に装入し、通常の条件で超高圧焼結すると、走査型電子顕微鏡による組織観察で、ｃ−ＢＮの硬質分散相とＴｉ炭・窒化物の連続結合相の間にＴｉ−Ａｌ−Ｗ系炭窒ほう化物の中間相が介在した組織を有するｃ−ＢＮ基焼結材料が形成されるようになること。
【０００６】
（ｃ）上記（ｂ）のｃ−ＢＮ基焼結材料を、上記の原料粉末の配合割合を調整して、同じく走査型電子顕微鏡による組織観察で、
上記ｃ−ＢＮの硬質分散相：５０〜７０％、
上記Ｔｉ−Ａｌ−Ｗ系炭窒ほう化物の中間相：５〜１５％、
上記Ｔｉ炭・窒化物の連続結合相および不可避不純物：残り、
からなる組成をもつものとした状態で、切削工具切刃片として用いると、前記ｃ−ＢＮ基焼結材料の中間相を構成するＴｉ−Ａｌ−Ｗ系炭窒ほう化物が上記の通りｃ−ＢＮの硬質分散相は勿論のこと、Ｔｉ炭・窒化物の連続結合相とも強固に結合することから、これを高硬度焼入れ鋼や鋳鉄などの表面仕上加工を断続切削条件で行なうのに用いても、チッピング発生の原因となる前記硬質分散相の前記連続結合相からの剥離脱落が防止され、すぐれた切削性能を長期に亘って発揮するようになること。
以上（ａ）〜（ｃ）に示される研究結果が得られたのである。
【０００７】
この発明は、上記の研究結果にもとづいてなされたものであって、
（ａ）原料粉末として、ｃ−ＢＮ粉末と、Ｔｉ炭・窒化物粉末と、Ｔｉ−Ａｌ金属間化合物粉末と、ＷＣ粉末と、を用意し、これら原料粉末を所定の配合組成に配合し、混合し、プレス成形してなる圧粉体に、真空雰囲気中、９００〜１３００℃の範囲内の所定温度に所定時間保持の条件で反応処理を施して、硬質のｃ−ＢＮからなる硬質分散相がＴｉ−Ａｌ−Ｗ系炭窒ほう化物で強固に結合された組織を有する反応焼結材料を形成し、
（ｂ）上記（ａ）の反応焼結材料を粉砕して、粉砕後の個々の粉末を硬質のｃ−ＢＮの表面にＴｉ−Ａｌ−Ｗ系炭窒ほう化物が強固に結合してなる複合粉末とし、この複合粉末を２次原料粉末とし、これに別途用意したＴｉ炭・窒化物粉末を所定の割合に配合し、混合し、プレス成形してなる圧粉体を、真空雰囲気中、９００〜１３００℃の範囲内の所定温度に所定時間保持の条件で焼結して切刃片用予備焼結体とし、
（ｃ）ついで、上記予備焼結体を、別途用意したＷＣ基超硬合金製支持片と重ね合わせた状態で、通常の超高圧焼結装置に装入し、通常の条件で超高圧焼結すること、
（ｄ）以上（ａ）〜（ｃ）の工程により、走査型電子顕微鏡による組織観察で、ｃ−ＢＮからなる硬質分散相と、Ｔｉ炭・窒化物からなる連続結合相の間に、Ｔｉ−Ａｌ−Ｗ系炭窒ほう化物からなる中間相が介在した組織を示し、かつ面積％で、
上記硬質分散相：５０〜７０％、
上記中間相：５〜１５％、
上記連続結合相および不可避不純物：残り、
からなる組成を有するｃ−ＢＮ基焼結材料で構成してなる、すぐれた耐チッピング性を有するｃ−ＢＮ基焼結材料製切削工具切刃片の製造方法に特徴を有するものである。
【０００８】
なお、この発明の方法で製造された切削工具切刃片を構成するｃ−ＢＮ基焼結材料において、硬質分散相の割合を５０〜７０面積％としたのは、その割合が５０面積％未満では所望のすぐれた耐摩耗性を確保することができず、一方その割合が７０面積％を超えると、相対的に焼結性および強度向上に寄与するＴｉ炭・窒化物（連続結合相）の割合が少なくなりすぎて切刃部に欠けが発生し易くなるという理由によるものであり、また、中間相の割合を５〜１５面積％と定めたのは、その割合が５面積％未満では硬質分散相および連続結合相との間に所望のすぐれた結合性を確保することができず、この結果切刃部にチッピングの発生が避けられず、一方その割合が１５面積％を超えると、ｃ−ＢＮ基焼結材料自体の強度が低下し、切刃部に欠けが発生し易くなるという理由からである。
【０００９】
【発明の実施の形態】
つぎに、この発明の切削工具切刃片の製造方法を実施例により具体的に説明する。
まず、原料粉末として、いずれも０．５〜４μｍの範囲内の平均粒径を有するｃ−ＢＮ粉末、Ｔｉ炭・窒化物粉末であるＴｉＣ粉末、ＴｉＮ粉末、およびＴｉＣＮ粉末、Ｔｉ−Ａｌ金属間化合物粉末であるＴｉ3Ａｌ粉末、ＴｉＡｌ粉末、およびＴｉＡｌ3粉末、さらにＷＣ粉末を用意し、これら原料粉末を表１に示される配合組成に配合し、ボールミルで７２時間湿式混合し、乾燥した後、１００ＭＰａの圧力で３０ｍｍ×３０ｍｍ×１０ｍｍの寸法をもった圧粉体にプレス成形し、ついでこの圧粉体に、圧力：１Ｐａの真空雰囲気中、９００〜１３００℃の範囲内の所定温度に３０分間保持の条件で反応処理を施して、硬質のｃ−ＢＮからなる硬質分散相がＴｉ−Ａｌ−Ｗ系炭窒ほう化物で強固に結合された組織を有する反応焼結材料Ａ〜Ｊを製造した。
【００１０】
ついで、上記反応焼結材料Ａ〜Ｊを粉砕して、粉砕後の個々の粉末を硬質のｃ−ＢＮの表面にＴｉ−Ａｌ−Ｗ系炭窒ほう化物が強固に結合してなる複合粉末とした状態で、これに別途用意した同じく０．５〜４μｍの範囲内の平均粒径を有するＴｉ炭・窒化物粉末であるＴｉＣ粉末、ＴｉＮ粉末、およびＴｉＣＮ粉末を表２に示される割合で配合し、ボールミルで４８時間湿式混合し、乾燥した後、１００ＭＰａの圧力で直径：４０ｍｍ×厚さ：２ｍｍの寸法をもった圧粉体にプレス成形し、ついでこの圧粉体に、圧力：１Ｐａの真空雰囲気中、９００〜１３００℃の範囲内の所定温度に３０分間保持の条件で焼結を施して切刃片用予備焼結体とし、この予備焼結体を、別途用意した、Ｃｏ：８質量％、ＷＣ：残りの組成、並びに直径：４０ｍｍ×厚さ：２．５ｍｍの寸法をもったＷＣ基超硬合金製支持片と重ね合わせた状態で、通常の超高圧焼結装置に装入し、通常の条件である圧力：５ＧＰａ、温度：１２００〜１４００℃の範囲内の所定温度、保持時間：０．５時間の条件で超高圧焼結し、焼結後上下面を研摩し、ワイヤー放電加工装置にて十字切断して４分割し、さらにこれに仕上げ研摩を施すことにより本発明法を実施し、本発明切削工具切刃片１〜１０をそれぞれ製造した。
【００１１】
また、比較の目的で、原料粉末として、上記の本発明切削工具切刃片１〜１０の製造に用いたと同じｃ−ＢＮ粉末、ＴｉＣ粉末、ＴｉＮ粉末、およびＴｉＣＮ粉末を用い、これら原料粉末を表３に示される配合組成に配合する以外は同一の条件で従来法を実施し、従来切削工具切刃片１〜６をそれぞれ製造した。
【００１２】
上記の本発明切削工具切刃片１〜１０および従来切削工具切刃片１〜６について、走査型電子顕微鏡およびオージェ分析装置を用いて組織観察したところ、それぞれ表２、３に示される組成を示し、かつ前者では、いずれもｃ−ＢＮの硬質分散相とＴｉ炭・窒化物の連続結合相の間にＴｉ−Ａｌ−Ｗ系炭窒ほう化物の中間相が介在した組織を示し、また後者では、いずれもｃ−ＢＮの硬質分散相とＴｉ炭・窒化物の連続結合相からなる組織を示した。
【００１３】
ついで、これらの本発明切削工具切刃片１〜１０および従来切削工具切刃片１〜６について、それぞれＣｏ：５質量％、ＴａＣ：５質量％、ＷＣ：残りの組成およびＣＩＳ規格ＴＮＧＡ３３２の形状（厚さ：３．１８mm×一辺長さ：１６mmの正三角形）をもったＷＣ基超硬合金製チップ本体のろう付け部（コーナー部）に、質量％で、Ｃｕ：３０％、Ｚｎ：２８％、Ｎｉ：２％、Ａｇ：残りからなる組成を有するＡｇ合金のろう材を用いてろう付けした状態で、
被削材：ＳＣＭ４１５の浸炭焼き入れ材（硬さＨR Ｃ：６０）の長さ方向等間隔４本縦溝入り丸棒、
切削速度：３００ｍ／ｍｉｎ．、
送り：０．２ｍｍ／ｒｅｖ．、
切り込み：０．５ｍｍ、
切削時間：４０分、
の条件での浸炭焼き入れ鋼の乾式断続表面仕上加工を行ない、切刃片の逃げ面摩耗幅を測定した。これらの測定結果を表２，３に示した。
【００１４】
【表１】
【表２】
【表３】
【発明の効果】
表２，３に示される結果から、本発明法で製造された本発明切削工具切刃片１〜１０は、いずれもこれを構成するｃ−ＢＮ基焼結材料がｃ−ＢＮの硬質分散相とＴｉ炭・窒化物の連続結合相の間にＴｉ−Ａｌ−Ｗ系炭窒ほう化物の中間相が介在した組織をもつことから、高硬度焼入れ鋼や鋳鉄などの表面仕上加工を断続切削条件で行なった場合にも、すぐれた耐チッピング性を示し、長期に亘ってすぐれた耐摩耗性を発揮するのに対して、従来法で製造された、前記Ｔｉ−Ａｌ−Ｗ系炭窒ほう化物からなる中間相の介在がないｃ−ＢＮ基焼結材料で構成された従来切削工具切刃片１〜６は、いずれもチッピングの発生によって、比較的短時間で使用寿命に至ることが明らかである。
上述のように、この発明の方法で製造された切削工具切刃片は、高硬度焼入れ鋼や鋳鉄などの表面仕上加工を連続切削条件で行なった場合は勿論のこと、断続切削条件で行なった場合にも、すぐれた耐チッピング性を示し、長期に亘ってすぐれた耐摩耗性を発揮するものであるから、切削加工の多様化、省力化、および省エネ化、さらに低コスト化に十分満足に対応できるものである。[0001]
BACKGROUND OF THE INVENTION
The present invention provides a cubic boron nitride (hereinafter referred to as c-BN) base that exhibits excellent chipping resistance even when surface finishing of hardened hardened steel or cast iron is performed under intermittent cutting conditions. The present invention relates to a method for manufacturing a cutting tool cutting piece made of a sintered material.
[0002]
[Prior art]
Conventionally, as a cutting tool generally using a c-BN-based sintered material as a cutting edge piece, for example, as described in an example of Japanese Patent Publication No. 1-16884, a cutting tool made of a c-BN-based sintered material is used. A composite composed of a blade piece or a cutting piece of a c-BN-based sintered material and a support piece of a WC-based cemented carbide is manufactured using a normal ultra-high pressure sintering apparatus. A brazing material of an Ag alloy having a composition containing, for example, Cu: 30%, Zn: 28%, Ni: 2%, and the balance of Ag and inevitable impurities in the cutting edge portion of the tool body made of Cutting tools made by brazing are widely known. These are throwaway inserts (hereinafter simply referred to as inserts) and drills, as well as cutting tools for end mills and reamers, such as hard-hardened steel and cast iron surfaces. Used in continuous cutting conditions for finishing Rukoto is where, which is also well known.
Further, as described above, as described in, for example, JP-A-56-156338, as a cutting tool cutting piece, a hard dispersed phase composed of c-BN, titanium carbide, nitride Consists of a continuous bonded phase composed of one or more of titanium and titanium carbonitride (hereinafter referred to as TiC, TiN, and TiCN, respectively) (hereinafter collectively referred to as Ti charcoal / nitride). The identified organization, and
The hard dispersed phase: 50 to 70 area%,
Above continuous bonded phase and inevitable impurities: remaining,
A cutting tool cutting edge piece made of a c-BN-based sintered material having a composition consisting of:
[0003]
[Problems to be solved by the invention]
On the other hand, cutting in recent years has been diversified in conjunction with higher performance of cutting devices, and there has been a strong demand for labor saving and energy saving of cutting processing, and further cost reduction. However, the above-mentioned conventional c-BN-based sintered material cutting tool cutting edge piece is used to perform surface finishing under continuous cutting conditions. However, if this is used for surface finishing under intermittent cutting conditions, the adhesion between the hard dispersed phase and the continuous bonded phase is not sufficient so that a peeling phenomenon occurs in the hard dispersed phase. As a result, chipping (small chipping) occurs at the cutting edge due to this, and the service life is reached in a relatively short time.
[0004]
[Means for Solving the Problems]
Therefore, the present inventors have focused on the above-mentioned conventional c-BN-based sintered material cutting tool cutting piece from the above viewpoint, and as a result of conducting research to improve its chipping resistance,
(A) First, c-BN powder, Ti charcoal / nitride powder, Ti-Al alloy powder, desirably Ti-Al intermetallic compound powder, and tungsten carbide (hereinafter referred to as WC) powder are prepared as raw material powder. These raw material powders are mixed in a predetermined composition and mixed, then pressed into a green compact, and then the green compact is subjected to a predetermined temperature within a range of 900 to 1300 ° C. in a vacuum atmosphere for a predetermined time. When the reaction treatment is performed under the holding conditions, the c-BN powder in the green compact is excellent in thermal stability, so that it does not substantially react by the sintering treatment and remains as it is. -Al alloy powder and WC powder react, and these also react with the surface portion of the c-BN powder to form a Ti-Al-W carbonitride, thus a hard material composed of extremely hard c-BN. Dispersed phase is Ti-Al To become possible as reaction sintering a material having a W-based carbonitride boride in tightly bound tissue is formed.
[0005]
(B) The reaction-sintered material of (a) is pulverized, and the individual powders after pulverization are firmly bonded to the surface of extremely hard c-BN with Ti-Al-W carbonitride. This composite powder is used as a secondary raw material powder, and Ti charcoal / nitride powder separately prepared is mixed in a predetermined ratio, mixed, and then pressed into a green compact at a predetermined pressure. The green compact is sintered in a vacuum atmosphere at a predetermined temperature in the range of 900 to 1300 ° C. for a predetermined time and is used as a primary sintered material. However, when ultra-high pressure sintering is performed under normal conditions, a Ti—Al—W-based carbonitride is observed between the hard dispersed phase of c-BN and the continuous bonded phase of Ti charcoal / nitride by microstructure observation with a scanning electron microscope. C-BN-based sintered material having a structure in which an intermediate phase of a chemical compound is interposed.
[0006]
(C) The above-mentioned c-BN-based sintered material (b) is adjusted by adjusting the blending ratio of the raw material powder, and the structure is similarly observed with a scanning electron microscope.
C-BN hard dispersed phase: 50-70%,
Intermediate phase of the Ti-Al-W carbonitride: 5-15%,
Ti Ti charcoal / nitride continuous binder phase and inevitable impurities: remaining,
Ti-Al-W-based carbonitrides that constitute the intermediate phase of the c-BN-based sintered material are c- BN is firmly bonded to the continuous bonded phase of Ti charcoal / nitride as well as the hard dispersed phase of BN, so it is used for surface finishing of hardened steel and cast iron under intermittent cutting conditions. However, peeling off of the hard dispersed phase from the continuous bonded phase, which causes chipping, is prevented, and excellent cutting performance is exhibited over a long period of time.
The research results shown in (a) to (c) above were obtained.
[0007]
This invention was made based on the above research results,
(A ) As a raw material powder, c-BN powder, Ti charcoal / nitride powder, Ti-Al intermetallic compound powder, and WC powder are prepared, and these raw material powders are blended in a predetermined blending composition, The green compact obtained by mixing and press-molding is subjected to a reaction treatment in a vacuum atmosphere at a predetermined temperature in the range of 900 to 1300 ° C. for a predetermined time, and a hard dispersed phase comprising hard c-BN. Forming a reaction sintered material having a structure tightly bonded with Ti-Al-W carbonitride,
(B) A composite in which the reaction sintered material of (a) is pulverized, and the individual powders after pulverization are firmly bonded to the surface of hard c-BN with Ti-Al-W carbonitride. The composite powder is used as a secondary raw material powder, and Ti charcoal / nitride powder separately prepared in the powder is mixed in a predetermined ratio, mixed, and press-molded into a green compact in a vacuum atmosphere. Sintered at a predetermined temperature within a range of ˜1300 ° C. for a predetermined time to obtain a pre-sintered body for a cutting blade piece,
(C) Next, the above pre-sintered body is placed in an ordinary ultra-high pressure sintering apparatus in a state of being superposed on a separately prepared WC-based cemented carbide support piece, and ultra-high pressure sintering is performed under normal conditions. To do,
(D) Through the steps (a) to (c) described above, between the hard dispersed phase composed of c-BN and the continuous bonded phase composed of Ti charcoal / nitride in the structure observation with a scanning electron microscope, Ti— An intermediate phase composed of an Al—W-based carbonitride is shown, and in area%,
The hard dispersed phase: 50 to 70%,
Intermediate phase: 5-15%
Above continuous bonded phase and inevitable impurities: remaining,
It becomes constituted by c-BN based sintered material having a composition consisting of, those characterized by a method for producing a c-BN based sintered material cutting tool made cutting piece having excellent chipping resistance.
[0008]
In the c-BN-based sintered material constituting the cutting tool cutting piece produced by the method of the present invention, the ratio of the hard dispersed phase is set to 50 to 70 area%, and the ratio is less than 50 area%. In this case, the desired excellent wear resistance cannot be ensured. On the other hand, when the proportion exceeds 70 area%, Ti charcoal / nitride (continuous binder phase) contributes relatively to improvement of sinterability and strength. This is because the ratio becomes too small and the cutting edge portion is likely to be chipped. The reason why the ratio of the intermediate phase is set to 5 to 15% by area is hard if the ratio is less than 5% by area. If the desired excellent bondability between the dispersed phase and the continuous bonded phase cannot be ensured, and as a result, the occurrence of chipping in the cutting edge cannot be avoided, while if the ratio exceeds 15 area%, c -The strength of the BN-based sintered material itself decreases, and the cutting edge It is the reason that the injury occur easily.
[0009]
DETAILED DESCRIPTION OF THE INVENTION
Next, the manufacturing method of the cutting tool cutting edge piece of the present invention will be specifically described with reference to examples.
First, as raw material powders, all are c-BN powders having an average particle diameter in the range of 0.5 to 4 μm, Ti carbon powders that are Ti charcoal / nitride powders, TiN powders, and TiCN powders, between Ti-Al metals After preparing compound powder Ti 3 Al powder, TiAl powder, TiAl 3 powder, and WC powder, these raw material powders are blended in the blending composition shown in Table 1, wet-mixed by a ball mill for 72 hours, and dried. , Pressed into a green compact having a size of 30 mm × 30 mm × 10 mm at a pressure of 100 MPa, and then pressed to a predetermined temperature within a range of 900 to 1300 ° C. in a vacuum atmosphere at a pressure of 1 Pa. Reactive sintered materials A to A having a structure in which a hard dispersion phase composed of hard c-BN is firmly bonded with a Ti-Al-W carbonitride for the reaction treatment under the condition of holding for a minute. It was prepared.
[0010]
Next, the above-mentioned reaction sintered materials A to J are pulverized, and the individual powders after pulverization are combined with a composite powder in which Ti-Al-W carbonitride is firmly bonded to the surface of hard c-BN. In this state, separately prepared TiC powder, TiN powder, and TiCN powder, which are Ti charcoal / nitride powders having an average particle size in the range of 0.5 to 4 μm, prepared separately, in the proportions shown in Table 2. The mixture was wet-mixed for 48 hours in a ball mill, dried, and then pressed into a green compact having a diameter of 40 mm × thickness: 2 mm at a pressure of 100 MPa. In a vacuum atmosphere, sintering was performed at a predetermined temperature within a range of 900 to 1300 ° C. for 30 minutes to obtain a pre-sintered body for a cutting edge piece, and this pre-sintered body was prepared separately, Co: 8 % By mass, WC: remaining composition and diameter: 40 m m × thickness: WC based cemented carbide support piece having dimensions of 2.5 mm, and placed in a normal ultra-high pressure sintering apparatus, under normal conditions of pressure: 5 GPa, temperature : Sintered under high pressure at a predetermined temperature in the range of 1200 to 1400 ° C and holding time: 0.5 hour. After sintering, the upper and lower surfaces are polished, cross-cut with a wire electric discharge machine, and divided into four. Further, the method of the present invention was carried out by applying final polishing to this, and the cutting tool pieces 1 to 10 of the present invention were produced.
[0011]
For the purpose of comparison, the same c-BN powder, TiC powder, TiN powder, and TiCN powder as those used in the production of the cutting tool cutting pieces 1 to 10 of the present invention are used as the raw material powder. The conventional method was implemented on the same conditions except mix | blending with the compounding composition shown by Table 3, and the conventional cutting tool cutting-blade pieces 1-6 were each manufactured.
[0012]
When the structure of the cutting tool pieces 1 to 10 of the present invention and the conventional cutting tool pieces 1 to 6 was observed with a scanning electron microscope and an Auger analyzer, the compositions shown in Tables 2 and 3 were obtained. The former shows a structure in which an intermediate phase of Ti-Al-W carbonitride is interposed between a hard dispersed phase of c-BN and a continuous bonded phase of Ti charcoal / nitride, and the latter. In either case, a structure composed of a hard dispersed phase of c-BN and a continuous bonded phase of Ti charcoal / nitride is shown.
[0013]
Then, for these cutting tool pieces 1 to 10 of the present invention and the cutting pieces 1 to 6 of the conventional cutting tool, Co: 5% by mass, TaC: 5% by mass, WC: remaining composition and shape of CIS standard TNGA332, respectively. In a brazed portion (corner portion) of a WC-based cemented carbide chip body having a thickness of 3.18 mm × one side length of 16 mm, Cu: 30%, Zn: 28 %, Ni: 2%, Ag: In a state of brazing using a brazing material of an Ag alloy having a composition consisting of:
Work material: SCM415 carburizing and quenching material (hardness H R C: 60) in the longitudinal direction at equal intervals, 4 vertical grooved round bars,
Cutting speed: 300 m / min. ,
Feed: 0.2 mm / rev. ,
Cutting depth: 0.5mm,
Cutting time: 40 minutes
Carburized and hardened steel was subjected to dry interrupted surface finishing under the conditions described above, and the flank wear width of the cutting edge piece was measured. The measurement results are shown in Tables 2 and 3.
[0014]
[Table 1]
[Table 2]
[Table 3]
【The invention's effect】
From the results shown in Tables 2 and 3, the cutting tool pieces 1 to 10 of the present invention produced by the method of the present invention are all hard dispersed phases in which the c-BN-based sintered material constituting this is c-BN. Intermittent cutting conditions for surface finishing of hardened steel, cast iron, etc. due to a structure in which an intermediate phase of Ti-Al-W carbonitride is intervened between the continuous bonded phase of Ti and Ti charcoal / nitride The Ti-Al-W-based carbonitrides produced by the conventional method, while exhibiting excellent chipping resistance and excellent wear resistance over a long period of time, also when performed in It is clear that all of the conventional cutting tool cutting pieces 1 to 6 made of a c-BN-based sintered material having no intermediate phase consisting of the above reach the service life in a relatively short time due to the occurrence of chipping. is there.
As described above, the cutting tool cutting piece manufactured by the method of the present invention was subjected to interrupted cutting conditions as well as surface finishing of hardened steel and cast iron under continuous cutting conditions. Even in this case, it exhibits excellent chipping resistance and exhibits excellent wear resistance over a long period of time, so it is fully satisfactory for diversification of cutting, labor saving, energy saving, and cost reduction. It can respond.
Claims (1)
（ｂ）上記（ａ）の反応焼結材料を粉砕して、粉砕後の個々の粉末を硬質の立方晶窒化ほう素の表面にＴｉ−Ａｌ−Ｗ系炭窒ほう化物が強固に結合してなる複合粉末とし、この複合粉末を２次原料粉末とし、これに別途用意した炭化チタン粉末、窒化チタン粉末、および炭窒化チタン粉末のうちの１種または２種以上を所定の割合に配合し、混合し、プレス成形してなる圧粉体を、真空雰囲気中、９００〜１３００℃の範囲内の所定温度に所定時間保持の条件で焼結して切刃片用予備焼結体とし、
（ｃ）ついで、上記予備焼結体を、別途用意した炭化タングステン基超硬合金製支持片と重ね合わせた状態で、通常の超高圧焼結装置に装入し、通常の条件で超高圧焼結すること、
（ｄ）以上（ａ）〜（ｃ）の工程により、走査型電子顕微鏡による組織観察で、立方晶窒化ほう素からなる硬質分散相と、炭化チタン、窒化チタン、および炭窒化チタンのうちの１種または２種以上からなる連続結合相の間に、Ｔｉ−Ａｌ−Ｗ系炭窒ほう化物からなる中間相が介在した組織を示し、かつ面積％で、
上記硬質分散相：５０〜７０％、
上記中間相：５〜１５％、
上記連続結合相および不可避不純物：残り、
からなる組成を有する立方晶窒化ほう素基焼結材料で構成してなる、すぐれた耐チッピング性を有する立方晶窒化ほう素基焼結材料製切削工具切刃片の製造方法。(A ) As raw material powder, one or more of titanium carbide powder, titanium nitride powder, and titanium carbonitride powder, cubic boron nitride powder, Ti—Al intermetallic compound powder, and tungsten carbide Powder, and these raw material powders are mixed in a predetermined composition, mixed, and press-molded into a green compact, which is kept in a vacuum atmosphere at a predetermined temperature within a range of 900 to 1300 ° C. for a predetermined time. To form a reaction sintered material having a structure in which a hard dispersed phase composed of hard cubic boron nitride is firmly bonded with a Ti-Al-W carbonitride,
(B) The reaction sintered material of (a) above is pulverized, and the individual powders after pulverization are firmly bonded to the surface of hard cubic boron nitride with Ti—Al—W-based carbonitride. The composite powder is used as a secondary raw material powder, and one or more of titanium carbide powder, titanium nitride powder, and titanium carbonitride powder prepared separately are blended in a predetermined ratio. The green compact obtained by mixing and press-molding is sintered in a vacuum atmosphere at a predetermined temperature within a range of 900 to 1300 ° C. for a predetermined time to obtain a presintered body for a cutting edge piece.
(C) Next, the pre-sintered body is placed in a super-high pressure sintering apparatus in a state of being superposed on a separately prepared tungsten carbide base cemented carbide support piece, and ultra-high pressure sintering is performed under normal conditions. Conclude,
(D) Through the steps (a) to (c) described above, a hard dispersed phase composed of cubic boron nitride and one of titanium carbide, titanium nitride, and titanium carbonitride can be obtained by structural observation with a scanning electron microscope. A structure in which an intermediate phase composed of a Ti—Al—W carbonitride is interposed between continuous seed phases or two or more types of continuous bonded phases, and in area%,
The hard dispersed phase: 50 to 70%,
Intermediate phase: 5-15%
Above continuous bonded phase and inevitable impurities: remaining,
A method of manufacturing a cutting tool cutting piece made of a cubic boron nitride-based sintered material having excellent chipping resistance, comprising a cubic boron nitride-based sintered material having a composition of
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