JP3972294B2

JP3972294B2 - Surface coated cemented carbide cutting tool with excellent wear resistance with hard coating layer in high speed cutting

Info

Publication number: JP3972294B2
Application number: JP2002125553A
Authority: JP
Inventors: 夏樹一宮; 隆史藤澤; 一樹泉; 秀充高岡
Original assignee: Mitsubishi Materials Corp
Current assignee: Mitsubishi Materials Corp
Priority date: 2002-04-26
Filing date: 2002-04-26
Publication date: 2007-09-05
Anticipated expiration: 2022-04-26
Also published as: JP2003311509A

Description

【０００１】
【発明の属する技術分野】
この発明は、硬質被覆層がすぐれた高温特性を有し、したがって特に各種の鋼や鋳鉄などの高熱発生を伴う高速切削加工で、すぐれた耐摩耗性を発揮する表面被覆超硬合金製切削工具（以下、被覆超硬工具という）に関するものである。
【０００２】
【従来の技術】
一般に、被覆超硬工具には、各種の鋼や鋳鉄などの被削材の旋削加工や平削り加工にバイトの先端部に着脱自在に取り付けて用いられるスローアウエイチップ、前記被削材の穴あけ切削加工などに用いられるドリルやミニチュアドリル、さらに前記被削材の面削加工や溝加工、肩加工などに用いられるソリッドタイプのエンドミルなどがあり、また前記スローアウエイチップを着脱自在に取り付けて前記ソリッドタイプのエンドミルと同様に切削加工を行うスローアウエイエンドミル工具などが知られている。
【０００３】
また、被覆超硬工具として、炭化タングステン（以下、ＷＣで示す）基超硬合金または炭窒化チタン（以下、ＴｉＣＮで示す）基サーメットからなる基体（以下、これらを総称して超硬基体と云う）の表面に、組成式：（Ａｌ_1-(X+Z)Ｔｉ_XＹ_Z）Ｎ（ただし、原子比で、Ｘは０．３５〜０．６０、Ｚ：０．００５〜０．１を示す）を満足するＡｌとＴｉとＹの複合窒化物［以下、（Ａｌ，Ｔｉ，Ｙ）Ｎで示す］層からなる硬質被覆層を１〜１５μｍの平均層厚で物理蒸着してなる被覆超硬工具が知られており、これが各種の鋼や鋳鉄などの連続切削や断続切削加工に用いられることも良く知られるところである。
【０００４】
さらに、上記の被覆超硬工具が、例えば図２に概略説明図で示される物理蒸着装置の１種であるアークイオンプレーティング装置に上記の超硬基体を装入し、ヒータで装置内を、例えば５００℃の温度に加熱した状態で、アノード電極と所定組成を有するＡｌ−Ｔｉ−Ｙ合金がセットされたカソード電極（蒸発源）との間に、例えば電流：９０Ａの条件でアーク放電を発生させ、同時に装置内に反応ガスとして窒素ガスを導入して、例えば２Ｐａの反応雰囲気とし、一方上記超硬基体には、例えば−１００Ｖのバイアス電圧を印加した条件で、前記超硬合金基体の表面に、上記（Ａｌ，Ｔｉ，Ｙ）Ｎ層からなる硬質被覆層を蒸着することにより製造されることも知られている。
【０００５】
【発明が解決しようとする課題】
近年の切削加工装置の高性能化はめざましく、一方で切削加工に対する省力化および省エネ化、さらに低コスト化の要求は強く、これに伴い、切削加工は高速化の傾向にあるが、上記の従来被覆超硬工具においては、これを通常の切削加工条件で用いた場合には問題はないが、これを高い発熱を伴う高速切削条件で用いた場合には、硬質被覆層が強度と靭性、さらに高温硬さと耐熱性（高温特性）を具備するものの、十分な高温特性具備するものでないために、硬質被覆層の摩耗進行が促進され、比較的短時間で使用寿命に至るのが現状である。
【０００６】
【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、特に高速切削加工ですぐれた耐摩耗性を発揮する被覆超硬工具を開発すべく、上記の従来被覆超硬工具を構成する硬質被覆層に着目し、研究を行った結果、
（ａ）上記の図２に示されるアークイオンプレーティング装置を用いて形成された従来被覆超硬工具を構成する（Ａｌ，Ｔｉ，Ｙ）Ｎ層は、層厚全体に亘って均質な高温硬さと耐熱性、および強度と靭性を有するが、例えば図１（ａ）に概略平面図で、同（ｂ）に概略正面図で示される構造のアークイオンプレーティング装置、すなわち装置中央部に超硬基体装着用回転テーブルを設け、前記回転テーブルを挟んで、一方側に上記の従来（Ａｌ，Ｔｉ，Ｙ）Ｎ層の形成に用いたと実質的に同じ組成のＡｌ−Ｔｉ−Ｙ合金、他方側には前記の従来Ａｌ−Ｔｉ−Ｙ合金に比して相対的にＴｉ含有量の低いＡｌ−Ｔｉ−Ｙ合金をいずれもカソード電極（蒸発源）として対向配置したアークイオンプレーティング装置を用い、この装置の前記回転テーブルの外周部に沿って複数の超硬基体をリング状に装着し、この状態で装置内雰囲気を窒素雰囲気として前記回転テーブルを回転させると共に、蒸着形成される硬質被覆層の層厚均一化を図る目的で超硬基体自体も自転させながら、前記の両側のカソード電極（蒸発源）とアノード電極との間にアーク放電を発生させて、前記超硬基体の表面に（Ａｌ，Ｔｉ，Ｙ）Ｎ層を形成すると、この結果の（Ａｌ，Ｔｉ，Ｙ）Ｎ層においては、回転テーブル上にリング状に配置された前記超硬基体が一方側の上記従来Ａｌ−Ｔｉ−Ｙ合金のカソード電極（蒸発源）に最も接近した時点で層中にＴｉ最高含有点が形成され、また前記超硬基体が上記の他方側の上記従来Ａｌ−Ｔｉ−Ｙ合金に比して相対的にＴｉ含有量が低いＡｌ−Ｔｉ−Ｙ合金のカソード電極に最も接近した時点で層中にＴｉ最低含有点が形成され、上記回転テーブルの回転によって層中には層厚方向にそって前記Ｔｉ最高含有点とＴｉ最低含有点が所定間隔をもって交互に繰り返し現れると共に、前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造をもつようになること。
【０００７】
（ｂ）上記（ａ）の繰り返し連続変化成分濃度分布構造の（Ａｌ，Ｔｉ，Ｙ）Ｎ層において、例えば対向配置のカソード電極（蒸発源）のそれぞれの組成を調製すると共に、超硬基体が装着されている回転テーブルの回転速度を制御して、
上記Ｔｉ最低含有点が、組成式：（Ａｌ_{1 -(X+Z)}Ｔｉ_XＹ_Z）Ｎ（ただし、原子比で、Ｘは０．０５〜０．３０、Ｚ：０．００５〜０．１を示す）、
上記Ｔｉ最高含有点が、組成式：（Ａｌ_1-(X+Z)Ｔｉ_XＹ_Z）Ｎ（ただし、原子比で、Ｘは０．３５〜０．５５、Ｚ：０．００５〜０．１を示す）、
をそれぞれ満足し、かつ隣り合う上記Ｔｉ最高含有点とＴｉ最低含有点の厚さ方向の間隔を０．０１〜０．１μmとすると、
上記Ｔｉ最低含有点部分では、上記の従来（Ａｌ，Ｔｉ，Ｙ）Ｎ層に比してＡｌ含有量が相対的に高くなることから、より一段とすぐれた高温硬さと耐熱性（高温特性）を示し、一方上記Ｔｉ最高含有点部分は、前記従来（Ａｌ，Ｔｉ，Ｙ）Ｎ層と同等の組成、すなわち前記Ｔｉ最低含有点部分に比して相対的にＡｌ含有量が低く、Ｔｉ含有量の高い組成をもつので、相対的に高い強度と靭性を保持し、かつこれらＴｉ最低含有点とＴｉ最高含有点の間隔をきわめて小さくしたことから、層全体の特性として強度と靭性を保持した状態で、著しくすぐれた高温特性を具備するようになり、したがって、硬質被覆層がかかる構成の（Ａｌ，Ｔｉ、Ｙ）Ｎ層からなる被覆超硬工具は、高い発熱を伴う鋼や鋳鉄などの高速切削加工ですぐれた耐摩耗性を発揮するようになること。
以上（ａ）および（ｂ）に示される研究結果を得たのである。
【０００８】
この発明は、上記の研究結果に基づいてなされたものであって、装置中央部に超硬基体装着用回転テーブルを設け、前記回転テーブルを挟んで、一方側にＴｉ最低含有点形成用Ａｌ−Ｔｉ−Ｙ合金、他方側にＴｉ最高含有点形成用Ａｌ−Ｔｉ−Ｙ合金をカソード電極（蒸発源）として対向配置したアークイオンプレーティング装置を用い、この装置の前記回転テーブルの外周部に沿って複数の超硬基体をリング状に装着し、この状態で装置内雰囲気を窒素雰囲気として前記回転テーブルを回転させると共に、超硬基体自体も自転させながら、前記の両側のカソード電極（蒸発源）とアノード電極との間にアーク放電を発生させて超硬基体の表面に、（Ａｌ，Ｔｉ，Ｙ）Ｎからなる硬質被覆層を１〜１５μｍの全体平均層厚で蒸着してなる被覆超硬工具にして、
上記硬質被覆層が、層厚方向にそって、Ｔｉ最低含有点とＴｉ最高含有点とが所定間隔をおいて交互に繰り返し存在し、かつ前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造を有し、
さらに、上記Ｔｉ最低含有点が、組成式：（Ａｌ_1-(X+Z)Ｔｉ_XＹ_Z）Ｎ（ただし、原子比で、Ｘは０．０５〜０．３０、Ｚ：０．００５〜０．１を示す）、
上記Ｔｉ最高含有点が、組成式：（Ａｌ_1-(X+Z)Ｔｉ_XＹ_Z）Ｎ（ただし、原子比で、Ｘは０．３５〜０．５５、Ｚ：０．００５〜０．１を示す）、
をそれぞれ満足し、かつ隣り合う上記Ｔｉ最高含有点とＴｉ最低含有点の間隔が、０．０１〜０．１μmである、
高速切削加工で硬質被覆層がすぐれた耐摩耗性を発揮する被覆超硬工具に特徴を有するものである。
【０００９】
つぎに、この発明の被覆超硬工具において、これを構成する硬質被覆層の構成を上記の通りに限定した理由を説明する。
（ａ）Ｔｉ最低含有点の組成
（Ａｌ，Ｔｉ，Ｙ）Ｎ層のＴｉ最低含有点におけるＡｌ成分は、高温硬さおよび耐熱性（高温特性）を向上させ、同Ｔｉ成分は強度および靭性を向上させ、さらに同Ｙ成分は一段と高温硬さを向上させる作用があり、したがってＡｌ成分およびＹ成分の含有割合が高くなればなるほど高温特性は向上したものになるので、高熱発生を伴う高速切削に適合したものになるが、Ｔｉの割合を示すＸ値がＡｌとＹの合量に占める割合（原子比）で０．０５未満になると、相対的にＴｉの割合が少な過ぎて、高強度および高靭性を有するＴｉ最高含有点が隣接して存在しても層自体の強度および靭性の低下は避けられず、この結果チッピングなどが発生し易くなり、一方Ｔｉの割合を示すＸ値が同０．３０を越えると、相対的にＡｌの割合が少なくなり過ぎて、高速切削に要求されるすぐれた高温特性を確保することができなくなるものであり、またＹ成分の割合を示すＺ値がＡｌとＴｉの合量に占める割合（原子比）で０．００５未満では所望の高温硬さ向上効果が得られず、さらに同Ｘ値が０．１を超えると、強度および靭性が急激に低下するようになることから、Ｘ値を０．０５〜０．３０、Ｚ値を０．００５〜０．１とそれぞれ定めた。
【００１０】
（ｂ）Ｔｉ最高含有点の組成
上記の通りＴｉ最低含有点は高温特性のすぐれたものであるが、反面強度および靭性の劣るものであるため、このＴｉ最低含有点の強度および靭性不足を補う目的で、上記の従来（Ａｌ，Ｔｉ，Ｙ）Ｎ層と同等の組成、すなわち相対的にＴｉ含有割合が高く、一方Ａｌ含有量が低く、これによって高強度および高靭性を有するようになるＴｉ最高含有点を厚さ方向に交互に介在させるものであり、したがってＴｉ成分の割合を示すＸ値がＡｌおよびＹ成分との合量に占める割合（原子比）で０．３５未満では、所望のすぐれた強度および靭性を確保することができず、一方同Ｘ値が０．５５を越えると、Ａｌに対するＴｉの割合が多くなり過ぎて、Ｔｉ最高含有点に所望のすぐれた高温特性を具備せしめることができなくなることから、Ｔｉ最高含有点でのＴｉ成分の割合を示すＸ値を０．３５〜０．５５と定めた。
また、Ｔｉ最高低含有点におけるＹ成分は、上記の通りＡｌ成分との共存で高温硬さを一段と向上させ、高熱発生を伴う高速切削に適合させる目的で含有するものであり、したがってＺ値が０．００５未満では所望の高温硬さ向上効果が得られず、一方Ｚ値が０．１を越えるとＴｉ最高含有点での強度および靭性に低下傾向が現れるようになることから、Ｚ値を０．００５〜０．１と定めた。
【００１１】
（ｃ）Ｔｉ最低含有点とＴｉ最高含有点間の間隔
その間隔が０．０１μm未満ではそれぞれの点を上記の組成で明確に形成することが困難であり、この結果層に所望の高温特性と強度および靭性を確保することができなくなり、またその間隔が０．１μmを越えるとそれぞれの点がもつ欠点、すなわちＴｉ最低含有点であれば靭性不足、Ｔｉ最高含有点であれば高温特性不足が層内に局部的に現れ、これが原因で切刃にチッピングが発生し易くなったり、摩耗進行が促進されるようになることから、その間隔を０．０１〜０．１μmと定めた。
【００１２】
（ｄ）硬質被覆層の全体平均層厚
その層厚が１μｍ未満では、所望の耐摩耗性を確保することができず、一方その平均層厚が１５μｍを越えると、切刃にチッピングが発生し易くなることから、その平均層厚を１〜１５μｍと定めた。
【００１３】
【発明の実施の形態】
つぎに、この発明の被覆超硬工具を実施例により具体的に説明する。
（実施例１）
原料粉末として、いずれも１〜３μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＶＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ₃Ｃ₂粉末、ＴｉＮ粉末、ＴａＮ粉末、およびＣｏ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の圧力で圧粉体にプレス成形し、この圧粉体を６Ｐａの真空中、温度：１４００℃に１時間保持の条件で焼結し、焼結後、切刃部分にＲ：０．０３のホーニング加工を施してＩＳＯ規格・ＣＮＭＧ１２０４０８のチップ形状をもったＷＣ基超硬合金製のチップ超硬基体Ａ−１〜Ａ−３，Ａ−５〜Ａ−１０を形成した。
【００１４】
また、原料粉末として、いずれも０．５〜２μｍの平均粒径を有するＴｉＣＮ（質量比で、ＴｉＣ／ＴｉＮ＝５０／５０）粉末、Ｍｏ₂Ｃ粉末、ＮｂＣ粉末、ＴａＣ粉末、ＷＣ粉末、Ｃｏ粉末、およびＮｉ粉末を用意し、これら原料粉末を、表２に示される配合組成に配合し、ボールミルで２４時間湿式混合し、乾燥した後、１００ＭＰａの圧力で圧粉体にプレス成形し、この圧粉体を２ｋＰａの窒素雰囲気中、温度：１５００℃に１時間保持の条件で焼結し、焼結後、切刃部分にＲ：０．０３のホーニング加工を施してＩＳＯ規格・ＣＮＭＧ１２０４０８のチップ形状をもったＴｉＣＮ系サーメット製のチップ超硬基体Ｂ−１〜Ｂ４，Ｂ−６を形成した。
【００１５】
ついで、上記のチップ超硬基体Ａ−１〜Ａ−３，Ａ−５〜Ａ−１０およびＢ−１〜Ｂ４，Ｂ−６のそれぞれを、アセトン中で超音波洗浄し、乾燥した状態で、図１に示されるアークイオンプレーティング装置内の回転テーブル上に外周部にそって装着し、一方側のカソード電極（蒸発源）として、種々の成分組成をもったＴｉ最低含有点形成用Ａｌ−Ｔｉ−Ｙ合金、他方側のカソード電極（蒸発源）として、種々の成分組成をもったＴｉ最高含有点形成用Ａｌ−Ｔｉ−Ｙ合金を前記回転テーブルを挟んで対向配置し、またボンバート洗浄用金属Ｔｉも装着し、まず装置内を排気して０．５Ｐａ以下の真空に保持しながら、ヒーターで装置内を５００℃に加熱した後、前記回転テーブル上で自転しながら回転する超硬基体に−１０００Ｖの直流バイアス電圧を印加し、かつカソード電極の前記金属Ｔｉとアノード電極との間に１００Ａの電流を流してアーク放電を発生させ、もって超硬基体表面をＴｉボンバート洗浄し、ついで装置内に反応ガスとして窒素ガスを導入して２Ｐａの反応雰囲気とすると共に、前記回転テーブル上で自転しながら回転する超硬基体に−１００Ｖの直流バイアス電圧を印加し、かつそれぞれのカソード電極(前記Ｔｉ最低含有点形成用Ａｌ−Ｔｉ−Ｙ合金およびＴｉ最高含有点形成用Ａｌ−Ｔｉ−Ｙ合金)とアノード電極との間に１００Ａの電流を流してアーク放電を発生させ、もって前記超硬基体の表面に、層厚方向に沿って表３に示される目標組成のＴｉ最低含有点とＴｉ最高含有点とが交互に同じく表３に示される目標間隔で繰り返し存在し、かつ前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造を有し、かつ同じく表３に示される目標全体層厚の硬質被覆層を蒸着することにより、本発明被覆超硬工具としての本発明表面被覆超硬合金製スローアウエイチップ（以下、本発明被覆超硬チップと云う）１〜１４をそれぞれ製造した。
【００１６】
また、比較の目的で、これらのチップ超硬基体Ａ−１〜Ａ−３，Ａ−５〜Ａ−１０およびＢ−１〜Ｂ４，Ｂ−６を、アセトン中で超音波洗浄し、乾燥した状態で、それぞれ図２に示される通常のアークイオンプレーティング装置に装入し、カソード電極（蒸発源）として種々の成分組成をもったＡｌ−Ｔｉ−Ｙ合金を装着し、さらにボンバート洗浄用金属Ｔｉも装着し、まず、装置内を排気して０．５Ｐａ以下の真空に保持しながら、ヒーターで装置内を５００℃に加熱した後、前記超硬基体に−１０００Ｖの直流バイアス電圧を印加し、カソード電極の前記金属Ｔｉとアノード電極との間に１００Ａの電流を流してアーク放電を発生させ、もって超硬基体表面をＴｉボンバート洗浄し、ついで装置内に反応ガスとして窒素ガスを導入して２Ｐａの反応雰囲気とすると共に、前記超硬基体に印加するバイアス電圧を−１００Ｖに下げて、前記カソード電極とアノード電極との間にアーク放電を発生させ、もって前記チップ超硬基体のそれぞれの表面に、表４に示される目標組成および目標層厚を有し、かつ層厚方向に沿って実質的に組成変化のない（Ａｌ，Ｔｉ，Ｙ）Ｎ層からなる硬質被覆層を蒸着することにより、従来被覆超硬工具としての従来表面被覆超硬合金製スローアウエイチップ（以下、従来被覆超硬チップと云う）１〜１４をそれぞれ製造した。
【００１７】
つぎに、上記本発明被覆超硬チップ１〜１４および従来被覆超硬チップ１〜１４について、これを工具鋼製バイトの先端部に固定治具にてネジ止めした状態で、
被削材：ＪＩＳ・ＳＣＭ４４０の丸棒、
切削速度：４００ｍ／ｍｉｎ．、
切り込み：２．０ｍｍ、
送り：０．２５ｍｍ／ｒｅｖ．、
切削時間：１０分、
の条件での合金鋼の乾式高速連続旋削加工試験、
被削材：ＪＩＳ・Ｓ４５Ｃの長さ方向等間隔４本縦溝入り丸棒、
切削速度：４００ｍ／ｍｉｎ．、
切り込み：２．０ｍｍ、
送り：０．２５ｍｍ／ｒｅｖ．、
切削時間：１０分、
の条件での炭素鋼の乾式高速断続旋削加工試験、さらに、
被削材：ＪＩＳ・ＦＣ３００の長さ方向等間隔４本縦溝入り丸棒、
切削速度：４００ｍ／ｍｉｎ．、
切り込み：２．５ｍｍ、
送り：０．２５ｍｍ／ｒｅｖ．、
切削時間：１０分、
の条件での鋳鉄の乾式高速断続旋削加工試験を行い、いずれの旋削加工試験でも切刃の逃げ面摩耗幅を測定した。この測定結果を表５に示した。
【００１８】
【表１】

【００１９】
【表２】

【００２０】
【表３】

【００２１】
【表４】

【００２２】
【表５】

【００２３】
（実施例２）
原料粉末として、平均粒径：５．５μｍを有する中粗粒ＷＣ粉末、同０．８μｍの微粒ＷＣ粉末、同１．３μｍのＴａＣ粉末、同１．２μｍのＮｂＣ粉末、同１．２μｍのＺｒＣ粉末、同２．３μｍのＣｒ₃Ｃ₂粉末、同１．５μｍのＶＣ粉末、同１．０μｍの（Ｔｉ，Ｗ）Ｃ粉末、および同１．８μｍのＣｏ粉末を用意し、これら原料粉末をそれぞれ表６に示される配合組成に配合し、さらにワックスを加えてアセトン中で２４時間ボールミル混合し、減圧乾燥した後、１００ＭＰａの圧力で所定形状の各種の圧粉体にプレス成形し、これらの圧粉体を、６Ｐａの真空雰囲気中、７℃／分の昇温速度で１３７０〜１４７０℃の範囲内の所定の温度に昇温し、この温度に１時間保持後、炉冷の条件で焼結して、直径が８ｍｍ、１３ｍｍ、および２６ｍｍの３種の超硬基体形成用丸棒焼結体Ｃ−１〜Ｃ−８を形成し、さらに前記の丸棒焼結体のうちの丸棒焼結体Ｃ−１，Ｃ−２，Ｃ−４〜Ｃ−８を用い、これから、研削加工にて、表６に示される組合せで、切刃部の直径×長さがそれぞれ６ｍｍ×１３ｍｍ、１０ｍｍ×２２ｍｍ、および２０ｍｍ×４５ｍｍの寸法を有し、かついずれもねじれ角：３０度の４枚刃スクエア形状をもったエンドミル超硬基体をそれぞれ製造した。
【００２４】
ついで、これらのエンドミル超硬基体の表面をアセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、層厚方向に沿って表７に示される目標組成のＴｉ最低含有点とＴｉ最高含有点とが交互に同じく表７に示される目標間隔で繰り返し存在し、かつ前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造を有し、かつ同じく表７に示される目標全体層厚の硬質被覆層を蒸着することにより、本発明被覆超硬工具としての本発明表面被覆超硬合金製エンドミル（以下、本発明被覆超硬エンドミルと云う）１〜７をそれぞれ製造した。
【００２５】
また、比較の目的で、上記のエンドミル超硬基体の表面をアセトン中で超音波洗浄し、乾燥した状態で、同じく図２に示される通常のアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、表８に示される目標組成および目標層厚を有し、かつ層厚方向に沿って実質的に組成変化のない（Ａｌ，Ｔｉ，Ｙ）Ｎ層からなる硬質被覆層を蒸着することにより、従来被覆超硬工具としての従来表面被覆超硬合金製エンドミル（以下、従来被覆超硬エンドミルと云う）１〜７をそれぞれ製造した。
【００２６】
つぎに、上記本発明被覆超硬エンドミル１〜７および従来被覆超硬エンドミル１〜７のうち、本発明被覆超硬エンドミル１，２および従来被覆超硬エンドミル１，２については、
被削材：平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＫＤ１１の板材、
切削速度：１５０ｍ／ｍｉｎ．、
溝深さ（切り込み）：３ｍｍ、
テーブル送り：６４０ｍｍ／分、
の条件での工具鋼の乾式高速溝切削加工試験、本発明被覆超硬エンドミル３〜５および従来被覆超硬エンドミル３〜５については、
被削材：平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＵＳ３０４の板材、
切削速度：１５０ｍ／ｍｉｎ．、
溝深さ（切り込み）：５ｍｍ、
テーブル送り：３８０ｍｍ／分、
の条件でのステンレス鋼の乾式高速溝切削加工試験、本発明被覆超硬エンドミル６，７および従来被覆超硬エンドミル６，７については、
被削材：平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＮＣＭ４３９の板材、
切削速度：２００ｍ／ｍｉｎ．、
溝深さ（切り込み）：１０ｍｍ、
テーブル送り：３２０ｍｍ／分、
の条件での合金鋼の乾式高速溝切削加工試験をそれぞれ行い、いずれの溝切削加工試験でも切刃部の外周刃の逃げ面摩耗幅が使用寿命の目安とされる０．１ｍｍに至るまでの切削溝長を測定した。この測定結果を表７、８にそれぞれ示した。
【００２７】
【表６】

【００２８】
【表７】

【００２９】
【表８】

【００３０】
（実施例３）
上記の実施例２で製造した直径が８ｍｍ、１３ｍｍ、および２６ｍｍの３種の丸棒焼結体のうちの丸棒焼結体Ｃ−１〜Ｃ−４，Ｃ−６〜Ｃ−８を用い、これから、研削加工にて、同じく表６に示される組合せで、溝形成部の直径×長さがそれぞれ４ｍｍ×１３ｍｍ、８ｍｍ×２２ｍｍ、および１６ｍｍ×４５ｍｍの寸法を有し、かついずれもねじれ角：３０度の２枚刃形状をもったドリル超硬基体をそれぞれ製造した。
【００３１】
ついで、これらのドリル超硬基体の切刃に、ホーニングを施し、アセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、層厚方向に沿って表９に示される目標組成のＴｉ最低含有点とＴｉ最高含有点とが交互に同じく表９に示される目標間隔で繰り返し存在し、かつ前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造を有し、かつ同じく表９に示される目標全体層厚の硬質被覆層を蒸着することにより、本発明被覆超硬工具としての本発明表面被覆超硬合金製ドリル（以下、本発明被覆超硬ドリルと云う）１〜７をそれぞれ製造した。
【００３２】
また、比較の目的で、上記のドリル超硬基体の表面に、ホーニングを施し、アセトン中で超音波洗浄し、乾燥した状態で、同じく図２に示される通常のアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、表１０に示される目標組成および目標層厚を有し、かつ層厚方向に沿って実質的に組成変化のない（Ａｌ，Ｔｉ，Ｙ）Ｎ層からなる硬質被覆層を蒸着することにより、従来被覆超硬工具としての従来表面被覆超硬合金製ドリル（以下、従来被覆超硬ドリルと云う）１〜７をそれぞれ製造した。
【００３３】
つぎに、上記本発明被覆超硬ドリル１〜７および従来被覆超硬ドリル１〜７のうち、本発明被覆超硬ドリル１〜３および従来被覆超硬ドリル１〜３については、
被削材：平面寸法：１００ｍｍ×２５０厚さ：５０ｍｍのＪＩＳ・ＳＫＤ６１の板材、
切削速度：１００ｍ／ｍｉｎ．、
送り：０．１５ｍｍ／ｒｅｖ、
穴深さ：１２ｍｍ
の条件での工具鋼の湿式高速穴あけ切削加工試験、本発明被覆超硬ドリル４，５および従来被覆超硬ドリル４，５については、
被削材：平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＦＣＤ４００の板材、
切削速度：１００ｍ／ｍｉｎ．、
送り：０．２５ｍｍ／ｒｅｖ、
穴深さ：２４ｍｍ
の条件でのダクタイル鋳鉄の湿式高速穴あけ切削加工試験、本発明被覆超硬ドリル６，７および従来被覆超硬ドリル６，７については、
被削材：平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＦＣ３００の板材、
切削速度：１１０ｍ／ｍｉｎ．、
送り：０．３０ｍｍ／ｒｅｖ、
穴深さ：５０ｍｍ
の条件での鋳鉄の湿式高速穴あけ切削加工試験、をそれぞれ行い、いずれの湿式高速穴あけ切削加工試験（水溶性切削油使用）でも先端切刃面の逃げ面摩耗幅が０．３ｍｍに至るまでの穴あけ加工数を測定した。この測定結果を表９、１０にそれぞれ示した。
【００３４】
【表９】

【００３５】
【表１０】

【００３６】
なお、この結果得られた本発明被覆超硬工具としての本発明被覆超硬チップ１〜１４、本発明被覆超硬エンドミル１〜７、および本発明被覆超硬ドリル１〜７を構成する硬質被覆層におけるＴｉ最低含有点とＴｉ最高含有点の組成、並びに従来被覆超硬工具としての従来被覆超硬チップ１〜１４、従来被覆超硬エンドミル１〜７、および従来被覆超硬ドリル１〜７の硬質被覆層の組成をオージェ分光分析装置を用いて測定したところ、それぞれ目標組成と実質的に同じ組成を示した。
また、これらの本発明被覆超硬工具の硬質被覆層におけるＴｉ最低含有点とＴｉ最高含有点間の間隔、およびこれの全体層厚、並びに従来被覆超硬工具の硬質被覆層の厚さを、走査型電子顕微鏡を用いて断面測定したところ、いずれも目標値と実質的に同じ値を示した。
【００３７】
【発明の効果】
表３〜１０に示される結果から、硬質被覆層が層厚方向にＴｉ最低含有点とＴｉ最高含有点とが交互に所定間隔をおいて繰り返し存在し、かつ前記Ｔｉ最高含有点から前記Ｔｉ最低含有点、前記Ｔｉ最低含有点から前記Ｔｉ最高含有点へＴｉ含有量が連続的に変化する成分濃度分布構造を有する本発明被覆超硬工具は、いずれも鋼や鋳鉄の切削加工を高い発熱を伴う高速で行っても、すぐれた耐摩耗性を発揮するのに対して、硬質被覆層が層厚方向に沿って実質的に組成変化のない（Ａｌ，Ｔｉ，Ｙ）Ｎ層からなる従来被覆超硬工具においては、高温を伴う高速切削加工では高温特性不足が原因で切刃の摩耗進行が速く、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、この発明の被覆超硬工具は、特に各種の鋼や鋳鉄などの高速切削加工でもすぐれた耐摩耗性を発揮し、長期に亘ってすぐれた切削性能を示すものであるから、切削加工装置の高性能化、並びに切削加工の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。
【図面の簡単な説明】
【図１】この発明の被覆超硬工具を構成する硬質被覆層を形成するのに用いたアークイオンプレーティング装置を示し、（ａ）は概略平面図、（ｂ）は概略正面図である。
【図２】従来被覆超硬工具を構成する硬質被覆層を形成するのに用いた通常のアークイオンプレーティング装置の概略説明図である。[0001]
BACKGROUND OF THE INVENTION
The present invention provides a surface-coated cemented carbide cutting tool that has a high temperature characteristic with a hard coating layer, and therefore exhibits excellent wear resistance particularly in high-speed cutting with high heat generation such as various steels and cast iron. (Hereinafter referred to as a coated carbide tool).
[0002]
[Prior art]
Generally, for coated carbide tools, a throw-away tip that is attached to the tip of a cutting tool for turning or flattening of various steel and cast iron work materials, and drilling of the work material. There are drills and miniature drills used for processing, etc., and solid type end mills used for chamfering, grooving, shoulder processing, etc. of the work material. A slow-away end mill tool that performs cutting work in the same manner as a type end mill is known.
[0003]
Further, as a coated carbide tool, a substrate made of tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet (hereinafter collectively referred to as a cemented carbide substrate). ) On the surface of the composition formula: (Al _{1-(X + Z)} Ti _X Y _Z ) N (wherein, in terms of atomic ratio, X is 0.35 to 0.60, Z is 0.005 to 0.1) A hard coating layer composed of a composite nitride of Al, Ti, and Y (hereinafter referred to as (Al, Ti, Y) N) satisfying the above condition is physically deposited with an average layer thickness of 1 to 15 μm. Hard tools are known, and it is well known that they are used for continuous cutting and intermittent cutting of various steels and cast irons.
[0004]
Furthermore, the above-mentioned coated carbide tool is, for example, the above-mentioned carbide substrate is inserted into an arc ion plating apparatus which is one type of physical vapor deposition apparatus schematically shown in FIG. For example, an arc discharge is generated between the anode electrode and a cathode electrode (evaporation source) on which an Al—Ti—Y alloy having a predetermined composition is set, for example, at a current of 90 A, while being heated to a temperature of 500 ° C. At the same time, nitrogen gas is introduced into the apparatus as a reaction gas to form a reaction atmosphere of, for example, 2 Pa, while the cemented carbide substrate has a surface of the cemented carbide substrate under the condition that a bias voltage of, for example, −100 V is applied. In addition, it is also known to be produced by vapor-depositing a hard coating layer composed of the (Al, Ti, Y) N layer.
[0005]
[Problems to be solved by the invention]
In recent years, the performance of cutting devices has been dramatically improved, while on the other hand, there is a strong demand for labor saving, energy saving, and cost reduction for cutting, and with this, cutting tends to be faster. In a coated carbide tool, there is no problem when it is used under normal cutting conditions, but when it is used under high-speed cutting conditions with high heat generation, the hard coating layer has strength and toughness. Although it has high temperature hardness and heat resistance (high temperature characteristics), it does not have sufficient high temperature characteristics, so that the progress of wear of the hard coating layer is promoted and the service life is reached in a relatively short time.
[0006]
[Means for Solving the Problems]
In view of the above, the present inventors have developed a hard coating layer that constitutes the above-described conventional coated carbide tool in order to develop a coated carbide tool that exhibits excellent wear resistance particularly in high-speed cutting. As a result of conducting research with a focus on
(A) The (Al, Ti, Y) N layer constituting the conventional coated carbide tool formed using the arc ion plating apparatus shown in FIG. 2 has a uniform high-temperature hardness over the entire thickness. For example, an arc ion plating apparatus having a structure shown in a schematic plan view in FIG. 1A and a schematic front view in FIG. A rotating table for mounting a substrate is provided, and an Al—Ti—Y alloy having substantially the same composition as that used for forming the conventional (Al, Ti, Y) N layer is disposed on one side across the rotating table, on the other side The arc ion plating apparatus in which both Al-Ti-Y alloys having a relatively low Ti content as compared with the conventional Al-Ti-Y alloy are arranged as cathode electrodes (evaporation sources) are used. The rotating table of this device A plurality of cemented carbide substrates are attached in a ring shape along the outer periphery of the steel plate. In this state, the rotary table is rotated with the atmosphere inside the apparatus as a nitrogen atmosphere, and the thickness of the hard coating layer formed by vapor deposition is made uniform. In order to achieve this, while rotating the carbide substrate itself, an arc discharge is generated between the cathode electrode (evaporation source) and the anode electrode on both sides, and (Al, Ti, Y) is formed on the surface of the carbide substrate. When the N layer is formed, in the resultant (Al, Ti, Y) N layer, the cemented carbide substrate arranged in a ring shape on the rotary table is the cathode electrode of the conventional Al-Ti-Y alloy on one side. At the point closest to the (evaporation source), the highest Ti content point is formed in the layer, and the cemented carbide substrate has a relatively higher Ti content than the conventional Al-Ti-Y alloy on the other side. Low Al-Ti-Y alloy cathode At the point closest to the pole, a Ti minimum content point is formed in the layer, and the rotation of the rotary table causes the Ti maximum content point and the Ti minimum content point to alternate in the layer thickness direction along the layer thickness direction. It repeatedly appears and has a component concentration distribution structure in which the Ti content continuously changes from the highest Ti content point to the lowest Ti content point and from the lowest Ti content point to the highest Ti content point.
[0007]
(B) In the (Al, Ti, Y) N layer of the repeated continuous change component concentration distribution structure of (a) above, for example, the respective compositions of the cathode electrodes (evaporation sources) arranged oppositely are prepared, and the carbide substrate is By controlling the rotation speed of the mounted rotary table,
The minimum Ti content point is the composition formula: (Al _{1-(X + Z)} Ti _X Y _Z ) N (however, in atomic ratio, X is 0.05 to 0.30, Z is 0.005 to 0.00. 1),
The Ti maximum content point, the composition _{formula: (Al 1- (X + Z} ) Ti X Y Z) N ( provided that an atomic ratio, X is 0.35~ 0.55, Z: 0.005~0. 1),
And the distance between the adjacent Ti highest content point and Ti lowest content point in the thickness direction is 0.01 to 0.1 μm,
Since the Al content is relatively higher than the conventional (Al, Ti, Y) N layer in the above-mentioned minimum Ti content point portion, the high temperature hardness and heat resistance (high temperature characteristics) are further improved. On the other hand, the Ti highest content point portion has the same composition as the conventional (Al, Ti, Y) N layer, that is, the Al content is relatively lower than the Ti lowest content point portion, and the Ti content Because it has a relatively high composition, it maintains relatively high strength and toughness, and the distance between these Ti minimum content point and Ti maximum content point is extremely small, so that the strength and toughness are maintained as the characteristics of the entire layer. Therefore, coated carbide tools composed of an (Al, Ti, Y) N layer with a hard coating layer are used for high-speed steel or cast iron with high heat generation. Excellent wear resistance in machining To become able to exert.
The research results shown in (a) and (b) above were obtained.
[0008]
The present invention was made based on the above research results, and provided with a carbide substrate mounting rotary table in the center of the apparatus, sandwiching the rotary table, and forming Ti minimum content point Al- Using an arc ion plating apparatus in which a Ti—Y alloy and an Al—Ti—Y alloy for forming the highest Ti content point on the other side are arranged to face each other as a cathode electrode (evaporation source), along the outer periphery of the rotary table of this apparatus A plurality of carbide substrates are mounted in a ring shape, and in this state, the atmosphere inside the apparatus is changed to a nitrogen atmosphere, the rotary table is rotated, and the carbide substrates themselves are rotated, while the cathode electrodes (evaporation sources) on both sides are rotated. and the surface of the carbide substrate by generating arc discharge between the anode electrode, formed by deposition (Al, Ti, Y) a hard coating layer made of N in total average layer thickness of 1~15μm coating In the hard tool,
In the hard coating layer, the lowest Ti content point and the highest Ti content point are alternately present at predetermined intervals along the layer thickness direction, and from the highest Ti content point to the lowest Ti content point, the Ti content A component concentration distribution structure in which the Ti content continuously changes from the lowest content point to the Ti highest content point,
Further, the minimum Ti content point is the composition formula: (Al _{1-(X + Z)} Ti _X Y _Z ) N (wherein, X is 0.05-0.30, Z: 0.005 in atomic ratio). 0.1)
The Ti maximum content point, the composition _{formula: (Al 1- (X + Z} ) Ti X Y Z) N ( provided that an atomic ratio, X is 0.35~ 0.55, Z: 0.005~0. 1),
And the interval between the adjacent highest Ti content point and the lowest Ti content point is 0.01 to 0.1 μm.
It is characterized by a coated carbide tool that exhibits excellent wear resistance with a hard coating layer in high-speed cutting.
[0009]
Next, in the coated carbide tool of the present invention, the reason why the structure of the hard coating layer constituting the tool is limited as described above will be described.
(A) Composition of the lowest Ti content point The Al component at the lowest Ti content point of the (Al, Ti, Y) N layer improves high temperature hardness and heat resistance (high temperature characteristics), and the Ti component improves strength and toughness. In addition, the Y component has the effect of further improving the high temperature hardness. Therefore, the higher the content ratio of the Al component and the Y component, the higher the high temperature characteristics, so it is suitable for high speed cutting with high heat generation. However, when the X value indicating the proportion of Ti is less than 0.05 in terms of the total amount of Al and Y (atomic ratio), the proportion of Ti is relatively small, and high strength and Even if the highest Ti content point having high toughness is present adjacently, a decrease in the strength and toughness of the layer itself is inevitable, and as a result, chipping and the like are likely to occur, while the X value indicating the Ti ratio is the same as 0. Over 30, phase In contrast, the proportion of Al becomes too small to ensure the excellent high temperature characteristics required for high speed cutting, and the Z value indicating the proportion of the Y component is the total amount of Al and Ti. If the proportion (atomic ratio) is less than 0.005, the desired high-temperature hardness improvement effect cannot be obtained, and if the X value exceeds 0.1, the strength and toughness will rapidly decrease. The X value was set to 0.05 to 0.30, and the Z value was set to 0.005 to 0.1.
[0010]
(B) Composition of highest Ti content point As described above, the lowest Ti content point has excellent high-temperature characteristics, but on the other hand, it is inferior in strength and toughness. For the purpose, the same composition as the above-mentioned conventional (Al, Ti, Y) N layer, that is, Ti having a relatively high Ti content, while the Al content is low, thereby having high strength and high toughness. The highest content point is alternately interposed in the thickness direction. Therefore, if the X value indicating the ratio of the Ti component is less than 0.35 in the ratio (atomic ratio) to the total amount of the Al and Y components, the desired content is obtained. While excellent strength and toughness cannot be ensured, on the other hand, if the X value exceeds 0.55 , the ratio of Ti with respect to Al increases so that the highest content point of Ti has desired excellent high temperature characteristics. Can From becoming impossible, it was defined as 0.35 to 0.55 the X value indicating a ratio of Ti component in Ti up containing point.
Further, the Y component at the highest Ti content point is contained for the purpose of further improving the high-temperature hardness in the coexistence with the Al component and adapting to high-speed cutting with high heat generation, and therefore the Z value is If it is less than 0.005, the desired high-temperature hardness improvement effect cannot be obtained. On the other hand, if the Z value exceeds 0.1, the strength and toughness at the highest Ti content point tend to decrease. It was determined to be 0.005 to 0.1.
[0011]
(C) Interval between the lowest Ti content point and the highest Ti content point If the distance is less than 0.01 μm, it is difficult to clearly form each point with the above composition. Strength and toughness cannot be ensured, and when the distance exceeds 0.1 μm, each point has defects, that is, if the Ti content is the lowest, the toughness is insufficient, and if the Ti content is the highest, the high temperature characteristics are insufficient. Since it appears locally in the layer and this makes it easier for chipping to occur on the cutting edge and promotes the progress of wear, the interval was set to 0.01 to 0.1 μm.
[0012]
(D) Overall average layer thickness of hard coating layer If the layer thickness is less than 1 μm, the desired wear resistance cannot be ensured, while if the average layer thickness exceeds 15 μm, chipping occurs on the cutting edge. Since it becomes easy, the average layer thickness was set to 1 to 15 μm.
[0013]
DETAILED DESCRIPTION OF THE INVENTION
Next, the coated carbide tool of the present invention will be specifically described with reference to examples.
Example 1
WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, TiN powder, TaN powder, and Co powder all having an average particle diameter of 1 to 3 μm are prepared as raw material powders. These raw material powders are blended in the composition shown in Table 1, wet mixed by a ball mill for 72 hours, dried, and then pressed into a green compact at a pressure of 100 MPa. Medium, sintered at 1400 ° C for 1 hour, after sintering, WC-based carbide with honing of R: 0.03 on the cutting edge and chip shape of ISO standard CNMG120408 Alloy chip carbide substrates A-1 to A-3, A-5 to A-10 were formed.
[0014]
In addition, as raw material powders, TiCN ( mass ratio, TiC / TiN = 50/50) powder, Mo ₂ C powder, NbC powder, TaC powder, WC powder, Co having an average particle diameter of 0.5 to 2 μm. Powder and Ni powder are prepared, these raw material powders are blended in the blending composition shown in Table 2, wet mixed by a ball mill for 24 hours, dried, and then pressed into a green compact at a pressure of 100 MPa. The green compact is sintered in a nitrogen atmosphere of 2 kPa at a temperature of 1500 ° C. for 1 hour. After sintering, the cutting edge portion is subjected to a honing process of R: 0.03, and an ISO standard / CNMG120408 chip Chip carbide substrates B-1 to B4 and B-6 made of TiCN cermet having a shape were formed.
[0015]
Next, each of the above chip carbide substrates A-1 to A-3, A-5 to A-10 and B-1 to B4, B-6 was ultrasonically cleaned in acetone and dried. Attached along the outer peripheral portion on the rotary table in the arc ion plating apparatus shown in FIG. 1, and used as a cathode electrode (evaporation source) on one side, Al— Ti-Y alloy, as the cathode electrode (evaporation source) on the other side, an Al-Ti-Y alloy for forming the highest Ti content point with various component compositions is placed facing each other across the rotary table, and for bombard cleaning. The metal Ti is also mounted. First, the inside of the apparatus is evacuated and kept at a vacuum of 0.5 Pa or less, and the inside of the apparatus is heated to 500 ° C. with a heater, and then rotated on the rotating table while rotating on the carbide substrate. -1000V DC A bias voltage is applied and a current of 100 A is passed between the metal Ti and the anode electrode of the cathode electrode to generate an arc discharge, thereby cleaning the surface of the carbide substrate with Ti bombardment, and then as a reaction gas in the apparatus. Nitrogen gas is introduced to form a reaction atmosphere of 2 Pa, a DC bias voltage of −100 V is applied to the carbide substrate rotating while rotating on the rotary table, and each cathode electrode (forms the lowest Ti content point) Al-Ti-Y alloy and Al-Ti-Y alloy for forming the highest Ti content point) and a current of 100 A are passed between the anode electrode and arc discharge is generated, so that a layer is formed on the surface of the carbide substrate. The lowest Ti content point and the highest Ti content point of the target composition shown in Table 3 along the thickness direction are alternately present at the target interval shown in Table 3 alternately, and The target total layer having a component concentration distribution structure in which the Ti content continuously changes from the highest Ti content point to the lowest Ti content point, from the lowest Ti content point to the highest Ti content point, and also shown in Table 3 By depositing a thick hard coating layer, throwaway tips made of the surface-coated cemented carbide of the present invention (hereinafter referred to as the present coated cemented carbide tips) 1 to 14 as the coated carbide tools of the present invention were produced.
[0016]
For comparison purposes, these chip superhard substrates A-1 to A-3, A-5 to A-10 and B-1 to B4, B-6 were ultrasonically cleaned in acetone and dried. In this state, each was loaded into the ordinary arc ion plating apparatus shown in FIG. 2, and an Al—Ti—Y alloy having various component compositions was mounted as a cathode electrode (evaporation source). Ti is also mounted. First, the inside of the apparatus is evacuated and kept at a vacuum of 0.5 Pa or less, and the inside of the apparatus is heated to 500 ° C. with a heater, and then a −1000 V DC bias voltage is applied to the carbide substrate. Then, a current of 100 A is passed between the metal Ti of the cathode electrode and the anode electrode to generate an arc discharge, thereby cleaning the surface of the carbide substrate with Ti bombardment, and then introducing nitrogen gas as a reaction gas into the apparatus. 2 with the reaction atmosphere of a, the lower the bias voltage applied to the carbide substrate to -100 V, the between the cathode electrode and the anode electrode to generate arc discharge, with each of the surface of said chip carbide substrate By vapor-depositing a hard coating layer composed of an (Al, Ti, Y) N layer having the target composition and target layer thickness shown in Table 4 and having substantially no composition change along the layer thickness direction. Then, conventional surface-coated cemented carbide throwaway tips (hereinafter referred to as conventional coated carbide tips) 1 to 14 as conventional coated carbide tools were produced.
[0017]
Next, with the present invention coated carbide tips 1-14 and the conventional coated carbide tips 1-14 , in a state where this is screwed to the tip of the tool steel tool with a fixing jig,
Work material: JIS / SCM440 round bar,
Cutting speed: 400 m / min. ,
Cutting depth: 2.0 mm
Feed: 0.25 mm / rev. ,
Cutting time: 10 minutes,
Dry high-speed continuous turning test of alloy steel under the conditions of
Work material: JIS · S45C lengthwise equal 4 round grooved round bars,
Cutting speed: 400 m / min. ,
Cutting depth: 2.0 mm
Feed: 0.25 mm / rev. ,
Cutting time: 10 minutes,
Carbon steel dry high-speed intermittent turning test,
Work material: JIS / FC300 lengthwise equidistant 4 bars with vertical grooves,
Cutting speed: 400 m / min. ,
Incision: 2.5mm,
Feed: 0.25 mm / rev. ,
Cutting time: 10 minutes,
A dry high-speed intermittent turning test of cast iron was performed under the conditions described above, and the flank wear width of the cutting edge was measured in any turning test. The measurement results are shown in Table 5 .
[0018]
[Table 1]

[0019]
[Table 2]

[0020]
[Table 3]

[0021]
[Table 4]

[0022]
[Table 5]

[0023]
(Example 2)
As raw material powders, medium coarse WC powder having an average particle diameter of 5.5 μm, fine WC powder of 0.8 μm, TaC powder of 1.3 μm, NbC powder of 1.2 μm, ZrC of 1.2 μm Prepare a powder, 2.3 μm Cr ₃ C ₂ powder, 1.5 μm VC powder, 1.0 μm (Ti, W) C powder, and 1.8 μm Co powder. Each of these was blended into the blending composition shown in Table 6 , further added with wax, ball milled in acetone for 24 hours, dried under reduced pressure, then pressed into various compacts of a predetermined shape at a pressure of 100 MPa. The green compact is heated to a predetermined temperature in the range of 1370 to 1470 ° C. at a rate of temperature increase of 7 ° C./min in a 6 Pa vacuum atmosphere, held at this temperature for 1 hour, and then fired under furnace cooling conditions. Finally, the diameters are 8mm, 13mm, and 26 Three carbide substrate for forming a round bar sintered C-1 through C-8 of the m forming, further round bar sintered C-1, C-2 of the round bar sintered body, Using C-4 to C-8, the diameters and lengths of the cutting edge portions are 6 mm × 13 mm, 10 mm × 22 mm, and 20 mm × 45 mm, respectively, in the combinations shown in Table 6 by grinding. Each of the end mill carbide substrates had a four-blade square shape with a twist angle of 30 degrees.
[0024]
Next, the surfaces of these end mill carbide substrates were ultrasonically cleaned in acetone, and in a dried state, they were charged into the arc ion plating apparatus shown in FIG. 1, and under the same conditions as in Example 1 above, A Ti minimum content point and a Ti maximum content point of the target composition shown in Table 7 along the layer thickness direction alternately and repeatedly exist at the target intervals shown in Table 7 , and from the Ti maximum content point to the Ti minimum content point. A hard coating layer having a component concentration distribution structure in which the Ti content continuously changes from the content point, the Ti minimum content point to the Ti maximum content point, and having the target total layer thickness shown in Table 7 is also deposited. it allows the present invention the surface coating cemented carbide end mill of the present invention coated cemented carbide (hereinafter, the present invention refers to the coating end mills) 1-7 were prepared, respectively.
[0025]
For the purpose of comparison, the surface of the above-mentioned end mill cemented carbide substrate was ultrasonically cleaned in acetone and dried, and then charged into the ordinary arc ion plating apparatus shown in FIG. 1. A hard coating layer composed of an (Al, Ti, Y) N layer having the target composition and target layer thickness shown in Table 8 and having substantially no composition change along the layer thickness direction under the same conditions as in Table 1. The conventional surface-coated cemented carbide end mills (hereinafter referred to as conventional coated carbide end mills) 1 to 7 as conventional coated carbide tools were produced respectively.
[0026]
Next, of the present invention coated carbide end mills 1 to 7 and the conventional coated carbide end mills 1 to 7 , the present coated carbide end mills 1 and 2 and the conventional coated carbide end mills 1 and 2 ,
Work material: Plane dimension: 100 mm × 250 mm, thickness: 50 mm JIS / SKD11 plate material,
Cutting speed: 150 m / min. ,
Groove depth (cut): 3 mm,
Table feed: 640 mm / min,
For the dry high-speed grooving test of tool steel under the conditions of the present invention, the coated carbide end mills 3-5 of the present invention and the conventional coated carbide end mills 3-5 ,
Work material: Plane dimension: 100 mm × 250 mm, thickness: 50 mm JIS / SUS304 plate,
Cutting speed: 150 m / min. ,
Groove depth (cut): 5 mm,
Table feed: 380 mm / min,
For the dry high-speed grooving test of stainless steel under the following conditions, the coated carbide end mills 6 and 7 of the present invention and the conventional coated carbide end mills 6 and 7 :
Work material: Plane dimension: 100 mm × 250 mm, thickness: 50 mm JIS / SNCM439 plate material,
Cutting speed: 200 m / min. ,
Groove depth (cut): 10 mm,
Table feed: 320 mm / min,
In each of the groove cutting tests, the flank wear width of the outer peripheral edge of the cutting edge reaches 0.1 mm, which is a guide for the service life. The cutting groove length was measured. The measurement results are shown in Tables 7 and 8 , respectively.
[0027]
[Table 6]

[0028]
[Table 7]

[0029]
[Table 8]

[0030]
(Example 3)
Using the round bar sintered bodies C-1 to C-4 and C-6 to C-8 among the three types of round bar sintered bodies having a diameter of 8 mm, 13 mm, and 26 mm manufactured in Example 2 above. , now at grinding, also in combinations shown in Table 6, the diameter × length 4 mm × 13 mm each of the groove forming portion has a size of 8 mm × 22 mm and 16 mm × 45 mm,, and both twist angle : Each drilled carbide substrate having a two-blade shape of 30 degrees was manufactured.
[0031]
Next, honing is performed on the cutting blades of these drill carbide substrates , ultrasonic cleaning in acetone is performed, and the dried state is inserted into the arc ion plating apparatus shown in FIG. Under the same conditions, the lowest Ti content point and the highest Ti content point of the target composition shown in Table 9 along the layer thickness direction are alternately present at the same target interval shown in Table 9 , and the highest Ti content. the Ti lowest containing from point containing point, the Ti minimum Ti content from content point to the Ti maximum content point has a continuously changing component concentration distribution structure, and also of the entire target layer thickness shown in Table 9 By vapor-depositing the hard coating layer, drills made of the surface-coated cemented carbide of the present invention (hereinafter referred to as the present invention coated carbide drill) 1 to 7 as the coated carbide tool of the present invention were produced.
[0032]
Further, for the purpose of comparison, honing is performed on the surface of the drill carbide substrate described above, ultrasonic cleaning is performed in acetone, and the state is dried, and then loaded into the normal arc ion plating apparatus shown in FIG. (Al, Ti, Y) N layer having the target composition and the target layer thickness shown in Table 10 and having substantially no composition change along the layer thickness direction under the same conditions as in Example 1 above. The conventional surface-coated cemented carbide drills (hereinafter referred to as conventional coated carbide drills) 1 to 7 as conventional coated carbide tools were produced by vapor-depositing a hard coating layer made of
[0033]
Next, of the present invention coated carbide drills 1-7 and conventional coated carbide drills 1-7 , the present invention coated carbide drills 1-3 and conventional coated carbide drills 1-3 are as follows:
Work material: Plane dimension: 100 mm x 250 Thickness: 50 mm JIS / SKD61 plate material,
Cutting speed: 100 m / min. ,
Feed: 0.15mm / rev,
Hole depth: 12mm
For the wet high speed drilling test of the tool steel under the conditions of the present invention, the coated carbide drills 4 and 5 of the present invention and the conventional coated carbide drills 4 and 5 ,
Work material: Plane dimension: 100 mm × 250 mm, thickness: 50 mm JIS / FCD400 plate material,
Cutting speed: 100 m / min. ,
Feed: 0.25mm / rev,
Hole depth: 24mm
For the wet high speed drilling test of ductile cast iron under the conditions of the present invention, the coated carbide drills 6 and 7 of the present invention and the conventional coated carbide drills 6 and 7 ,
Work material: Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / FC300 plate material,
Cutting speed: 110 m / min. ,
Feed: 0.30mm / rev,
Hole depth: 50mm
Wet cast high-speed drilling test of cast iron under the conditions of each, and any wet high-speed drilling cutting test (using water-soluble cutting oil) until the flank wear width of the cutting edge surface reaches 0.3mm The number of drilling operations was measured. The measurement results are shown in Tables 9 and 10 , respectively.
[0034]
[Table 9]

[0035]
[Table 10]

[0036]
In addition, the hard coating which comprises this invention coated carbide tip 1-14 as this invention coated carbide tool obtained as a result of this invention, this invention coated carbide end mill 1-7 , and this invention coated carbide drill 1-7 the composition of Ti lowest containing points and Ti maximum content point in the layer, as well as conventional coating hard tip 1-14 as a conventional coated cemented carbide tools, the conventional coated cemented carbide end mills 1-7, and the conventional coated cemented carbide drills 1-7 When the composition of the hard coating layer was measured using an Auger spectroscopic analyzer, the composition was substantially the same as the target composition.
Further, the interval between the Ti minimum content point and the Ti maximum content point in the hard coating layer of these coated carbide tools of the present invention, and the total layer thickness thereof, and the thickness of the hard coating layer of the conventional coated carbide tool, When the cross-section was measured using a scanning electron microscope, all showed substantially the same value as the target value.
[0037]
【The invention's effect】
From the results shown in Tables 3 to 10 , in the hard coating layer, the Ti lowest content point and the Ti highest content point are alternately repeated at predetermined intervals in the layer thickness direction, and the Ti lowest content point is from the Ti highest content point. The coated carbide tool of the present invention having a component concentration distribution structure in which the Ti content continuously changes from the content point, the Ti minimum content point to the Ti maximum content point, all of which produce high heat generation when cutting steel and cast iron. Conventional coating consisting of an (Al, Ti, Y) N layer in which the hard coating layer has substantially no composition change along the layer thickness direction while exhibiting excellent wear resistance even at high speeds In cemented carbide tools, it is clear that in high-speed cutting with high temperature, the wear of the cutting blade progresses rapidly due to insufficient high-temperature characteristics, and the service life is reached in a relatively short time.
As described above, the coated carbide tool of the present invention exhibits excellent wear resistance even in high-speed cutting such as various types of steel and cast iron, and exhibits excellent cutting performance over a long period of time. It is possible to satisfactorily cope with the high performance of the cutting device, the labor saving and energy saving of cutting, and the cost reduction.
[Brief description of the drawings]
FIG. 1 shows an arc ion plating apparatus used to form a hard coating layer constituting a coated carbide tool of the present invention, wherein (a) is a schematic plan view and (b) is a schematic front view.
FIG. 2 is a schematic explanatory view of a normal arc ion plating apparatus used to form a hard coating layer constituting a conventional coated carbide tool.

Claims

A rotating table for mounting either or both of a tungsten carbide-based cemented carbide substrate and a titanium carbonitride-based cermet substrate is provided in the center of the apparatus, and the Ti-containing point forming Al-- Using an arc ion plating apparatus in which a Ti—Y alloy and an Al—Ti—Y alloy for forming the highest Ti content point on the other side are arranged to face each other as a cathode electrode (evaporation source), along the outer periphery of the rotary table of this apparatus A plurality of the bases are mounted in a ring shape, and in this state, the atmosphere inside the apparatus is changed to a nitrogen atmosphere, the rotary table is rotated, and the base itself is rotated, while the cathode electrodes (evaporation sources) and the anodes on both sides are rotated. by generating arc discharge between the electrodes, the surface of the substrate, of 1~15μm a hard layer made of a composite nitride of Al, Ti, and Y In the surface-coated cemented carbide cutting tool formed by depositing the body average layer thickness,
In the hard coating layer, the lowest Ti content point and the highest Ti content point are alternately present at predetermined intervals along the layer thickness direction, and from the highest Ti content point to the lowest Ti content point, the Ti content A component concentration distribution structure in which the Ti content continuously changes from the lowest content point to the Ti highest content point,
Furthermore, the Ti lowest content point, the composition _{formula: (Al 1- (X + Z} ) Ti X Y Z) N ( provided that an atomic ratio, X is 0.05 to 0.30, Z: 0.005 to 0.1)
The Ti maximum content point, the composition _{formula: (Al 1- (X + Z} ) Ti X Y Z) N ( provided that an atomic ratio, X is 0.35~ 0.55, Z: 0.005~0. 1),
And the interval between the adjacent highest Ti content point and the lowest Ti content point is 0.01 to 0.1 μm,
A surface-coated cemented carbide cutting tool that exhibits excellent wear resistance with a hard coating layer in high-speed cutting.