JP3899501B2 - Cutting tool made of surface-coated carbide material that exhibits excellent wear resistance in high heat generation cutting - Google Patents
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Description
【０００１】
【発明の属する技術分野】
この発明は、特に高い熱発生を伴なう切削加工で硬質被覆層がすぐれた高温熱伝導性を発揮し、したがって例えば切刃が高温にさらされる高速切削に用いても切刃の摩耗進行が抑制され、長期に亘ってすぐれた耐摩耗性を発揮する表面被覆超硬材料製切削工具（以下、被覆超硬工具と云う）に関するものである。
【０００２】
【従来の技術】
従来、例えば図１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を用い、ヒータで装置内を例えば４００℃の温度に加熱した状態で、アノード電極と金属Ｔｉまたは金属Ａｌがセットされたカソード電極（蒸発源）との間にアーク放電を発生させ、同時に装置内に反応ガスとして、前記カソード電極に前記金属Ｔｉがセットされた場合にはメタンガス、窒素ガス、または窒素ガスとメタンガスを導入し、また前記金属Ａｌがセットされた場合には酸素ガスを導入し、一方炭化タングステン（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）系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）には、例えば−７０Ｖのバイアス電圧を印加した条件で、前記超硬基体の表面に、
（ａ）いずれも０．１〜５μｍの平均層厚を有し、かつそれぞれ組成式：ＴｉＣＥ 、ＴｉＮＥ 、およびＴｉ（Ｃ１−ＦＮＦ）Ｅ で表した場合、原子比でＥ：０．８〜１．２、Ｆ：０．３〜０．７を満足する炭化チタン層、窒化チタン層、および炭窒化チタン層のうちの１層または２層以上からなるＴｉ化合物層、
（ｂ）０．１〜１０μｍの平均層厚を有し、かつ、
組成式：ＡｌＯZ 、
で表した場合、原子比でＺ：１〜２を満足する酸化アルミニウム層（以下、ＡｌＯＺ層と云う）、
以上（ａ）および（ｂ）で構成された硬質被覆層を０．５〜２０μｍの全体平均層厚で物理蒸着してなる被覆超硬工具を製造することが試みられ、かつ実用化のための研究が行われている。
【０００３】
【発明が解決しようとする課題】
一方、近年の切削装置の高性能化および高出力化はめざましく、かつ切削加工の省力化および省エネ化に対する要求もつよく、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、これを高い熱発生を伴なう高速切削に用いた場合、硬質被覆層を構成するＴｉ化合物層はすぐれた高温熱伝導性を示すものの、同ＡｌＯＺ層は高温にさらされると熱伝導性が急激に低下することから、切刃の温度上昇が避けられず、これが原因で摩耗進行が促進されるようになり、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、高熱発生切削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研究を行った結果、
上記の従来被覆超硬工具の硬質被覆層を構成するＡｌＯＺ層に代わって、高温熱伝導性のすぐれた酸化ジルコニウム、すなわち組成式：ＺｒＯＺ（ただし、Ｚは、原子比で１．５〜２．５を示す）で表される酸化ジルコニウムを主体とし、これのＺｒの一部を、高温硬さ向上を目的として、Ｖ、Ｃｒ、およびＹのうちの１種（以下、Ｍで示す）で置換してなるＺｒ系複合酸化物からなる硬質被覆層、すなわち組成式：（Ｚｒ１−Ｘ ＭＸ ）ＯＺ（ただし、原子比でＸ：０．０１〜０．３、Ｚ：１．５〜２．５を示す）で表されるＺｒ系複合酸化物からなる硬質被覆層を、同じくＴｉ化合物層と共存させた状態で適用すると、この硬質被覆層がＺｒ系複合酸化物層とＴｉ化合物層とで構成された被覆超硬工具は、前記Ｚｒ系複合酸化物層およびＴｉ化合物層のもつすぐれた高温熱伝導性、さらに前記Ｚｒ系複合酸化物層のもつすぐれた高温硬さによって、これを高い発熱を伴なう例えば鋼などの高速切削に用いても、切刃の摩耗進行が抑制され、長期に亘ってすぐれた耐摩耗性を発揮するようになるという研究結果が得られたのである。
【０００５】
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、超硬基体の表面に、
（ａ）いずれも０．１〜５μｍの平均層厚を有し、かつそれぞれ組成式：ＴｉＣＥ 、ＴｉＮＥ 、およびＴｉ（Ｃ１−ＦＮＦ）Ｅ で表した場合、原子比でＥ：０．８〜１．２、Ｆ：０．３〜０．７を満足する炭化チタン層、窒化チタン層、および炭窒化チタン層のうちの１層または２層以上からなるＴｉ化合物層、
（ｂ）それぞれ個々の平均層厚が０．１〜１０μｍにして、かつ、
組成式：（Ｚｒ１−Ｘ ＭＸ ）ＯＺ 、
（ただし、ＭはＶ、Ｃｒ、およびＹのうちの１種からなる）、
で表した場合、原子比でＸ：０．０１〜０．３、Ｚ：１．５〜２．５を満足するＺｒ系複合酸化物層、
以上（ａ）および（ｂ）で構成された硬質被覆層を０．５〜２０μｍの全体平均層厚で物理蒸着してなる、高熱発生切削で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。
【０００６】
つぎに、この発明の被覆超硬工具において、硬質被覆層を構成するＴｉ化合物層およびＺｒ系複合酸化物層の組成式および平均層厚を上記の通りに限定した理由を説明する。
（ａ）Ｔｉ化合物層
Ｔｉ化合物層は、いずれも同じ構成層であるＺｒ系複合酸化物層に比して高温硬さは低いが、高い靭性を有し、もって硬質被覆層に所定の靭性を具備せしめるのに不可欠のものであり、これによって実用時に切刃に欠けやチッピング（微小欠け）などの欠損が発生するのを抑制する作用を発揮し、かつ相対硬さも窒化チタン層、炭窒化チタン層、および炭化チタン層の順に高くなるが、いずれもＺｒ系複合酸化物層と同等のすぐれた高温熱伝導性をもつものであり、しかし、その平均層厚が０．１μｍ未満では前記作用に所望の効果が得られず、一方前記作用は５μｍまでの平均層厚で十分であり、これ以上の層厚は不必要であることから、その平均層厚を０．１〜５μｍと定めた。
また、それぞれのＴｉ化合物層におけるＥ値は、その値が０．８未満になると層自体が軟質になりすぎて、耐摩耗性の低下が著しく、一方その値が１．２を越えると層が脆化するようになって欠損発生の原因となることから、Ｅ値を０．８〜１．２と定めている。
さらに、炭窒化チタン層におけるＦ値は、その値が０．３未満になっても、０．７を越えても窒化チタン層と炭化チタン層の中間的性質を保持できなくなることから、Ｆ値を０．３〜０．７と定めている。
【０００７】
（ｂ）Ｚｒ系複合酸化物層
同じく硬質被覆層を構成するＺｒ系複合酸化物層は、上記の通りＺｒＯＺ のもつすぐれた高温熱伝導性を保持した状態で、Ｍ成分によるすぐれた高温硬さを有し、もって高発熱切削時の耐摩耗性低下を抑制する作用を発揮するが、組成式におけるＭ成分のＺｒとの合量に占める割合を示すＸ値を原子比で０．０１〜０．３としたのは、Ｘ値が０．０１未満ではＺｒ系複合酸化物層の高温硬さに所望の向上効果が得られず、一方Ｘ値が０．３を越えると、特に靭性が急激に低下し、所望の切刃に欠けやチッピングなどの欠損が発生し易くなるという理由からであり、望ましくは０．０５〜０．２５のＸ値とするのがよい。
また、上記Ｚｒ系複合酸化物層におけるＺ値を原子比で１．５〜２．５と定めたのは、Ｚ値が１．５未満では相対的にＺｒに対する酸素の割合が少なくなりすぎて、所望のすぐれた高温熱伝導性を確保することができず、一方Ｚ値が２．５を越えると層自体が急激に脆化し、これが欠損発生の原因となるという理由にもとづくものである。
さらに、上記Ｚｒ系複合酸化物層の個々の平均層厚を０．１〜１０μｍとしたのは、その層厚が０．１μｍ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、一方その層厚が１０μｍを越えると切刃にチッピングが発生し易くなるという理由からであり、望ましくは０．２〜５．０μｍとするのがよい。
【０００８】
また、硬質被覆層の全体平均層厚を０．５〜２０μｍとしたのは、その層厚が０．５μｍ未満では硬質被覆層による耐摩耗性向上に所望の効果が得られず、一方その層厚が２０μｍを越えると切刃にチッピングが発生し易くなるという理由からであり、望ましくは３〜１０μｍの平均層厚とするのがよい。
【０００９】
【発明の実施の形態】
ついで、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。
原料粉末として、いずれも０．５〜３．５μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＴａＣ粉末、およびＣｏ粉末を用意し、これら原料粉末を、重量％でＷＣ：９０％、ＴｉＣ：１％、ＴａＣ：１％、Ｃｏ：８％の配合組成に配合し、ボールミルで７２時間湿式混合し、乾燥した後、１．５ｔｏｎ／ｃｍ2 の圧力で圧粉体にプレス成形し、この圧粉体を真空中、温度：１４５０℃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・ＳＥＫＮ１２０３ＡＦＥＮ１のチップ形状をもったＷＣ基超硬合金製の超硬基体Ａを形成した。
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［重量比で、ＴｉＣ／ＴｉＮ＝５０／５０］粉末、ＴａＣ粉末、ＷＣ粉末、ＶＣ粉末、Ｃｏ粉末、Ｎｉ粉末、および黒鉛（Ｃ）粉末を用意し、これら原料粉末を、重量％で、ＴｉＣＮ：７４．５％、ＴａＣ：３％、ＷＣ：９．５％、ＶＣ：１％、Ｃｏ：８％、Ｎｉ：３％、Ｃ：１％の配合組成に配合し、ボールミルで２４時間湿式混合し、乾燥した後、１ｔｏｎ／ｃｍ2 の圧力で圧粉体にプレス成形し、この圧粉体を５ｔｏｒｒ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・ＳＥＥＮ１２０３ＡＦＥＮ１のチップ形状をもったＴｉＣＮ系サーメット製の超硬基体Ｂを形成した。
【００１０】
ついで、これら超硬基体Ａ、Ｂ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、一方カソード電極（蒸発源）として種々の成分組成をもったＺｒ−Ｍ合金、金属Ｔｉ、さらに金属Ａｌをそれぞれ装着し、装置内を排気して１×１０-5ｔｏｒｒの真空に保持しながら、ヒーターで装置内を４００℃に加熱した後、超硬合金基体に−５０ｖのバイアス電圧を印加し、装置内に反応ガスとして、カソード電極を金属ＴｉとしてＴｉ化合物層を形成する場合には、メタンガス、窒素ガス、または窒素ガスとメタンガスを導入し、またカソード電極をＺｒ−Ｍ合金または金属ＡｌとしてＺｒ系複合酸化物層またはＡｌＯＺ層を形成する場合には酸素ガスを導入しながら、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、もって前記超硬合金基体Ａ、Ｂのそれぞれの表面に、表１〜３に示される目標組成および目標層厚の硬質被覆層を物理蒸着することにより、硬質被覆層がＴｉ化合物層とＺｒ系複合酸化物層で構成された本発明被覆超硬工具１〜７、および硬質被覆層がＴｉ化合物層とＡｌＯＺ 層で構成された従来被覆超硬工具１〜４をそれぞれ製造した。
なお、上記の各種の被覆超硬工具について、これの硬質被覆層の断面を走査型電子顕微鏡により観察し、その組成および層厚を測定したところ、表１〜３に示される目標組成および目標層厚と実質的に同じ組成および平均層厚を示した。
【００１１】
この結果得られた各種の被覆超硬工具のうち、本発明被覆超硬工具１〜４および従来被覆超硬合金工具１、２については、
被削材：ＪＩＳ・ＳＮＣＭ４３９（硬さ：ＨR Ｃ３０）の角材、
切削速度：２８０ｍ／ｍｉｎ、
送り：０．２ｍｍ／刃（単刃）、
切り込み：１．５ｍｍ、
切削時間：２５分、
の条件（切削条件Ａと云う）での合金鋼の乾式高速フライス切削試験、並びに、 被削材：ＪＩＳ・ＳＫＤ６１（硬さ：ＨR Ｃ６０）の角材、
切削速度：３００ｍ／ｍｉｎ、
送り：０．０８ｍｍ／刃（単刃）、
切り込み：１ｍｍ、
切削時間：１０分、
の条件（切削条件Ｂと云う）での焼き入れ鋼の乾式高速フライス切削試験を行ない、また本発明被覆超硬工具５〜７および比較被覆超硬工具３、４については、
被削材：ＪＩＳ・ＳＮＣＭ４３９（硬さ：ＨR Ｃ３２）の角材、
切削速度：３５０ｍ／ｍｉｎ、
送り：０．１５ｍｍ／刃（単刃）、
切り込み：１．５ｍｍ、
切削時間：２０分、
の条件（切削条件Ｃと云う）での合金鋼の乾式高速フライス切削試験、並びに、 被削材：ＪＩＳ・ＳＫＤ６１（硬さ：ＨR Ｃ５５）の角材、
切削速度：３２０ｍ／ｍｉｎ、
送り：０．１ｍｍ／刃（単刃）、
切り込み：１ｍｍ、
切削時間：１５分、
の条件（切削条件Ｄと云う）での焼き入れ鋼の乾式高速フライス切削試験を行ない、いずれの切削試験でも切刃の逃げ面摩耗幅を測定した。これらの測定結果を表２、３に示した。
【００１２】
【表１】
【表２】
【表３】
【発明の効果】
表１〜３に示される結果から、本発明被覆超硬工具１〜７は、いずれも硬質被覆層を構成するＺｒ系複合酸化物層およびＴｉ化合物層がすぐれた高温熱伝導性を有し、かつ前記Ｚｒ系複合酸化物層は高温硬さにすぐれ、また前記Ｔｉ化合物層は靭性にすぐれたものであることと相まって、刃先が高温加熱される高硬度鋼の高速切削にも前記硬質被覆層の熱伝導性の低下が抑制され、刃先の過熱が防止されることから、すぐれた耐摩耗性を示し、かつ切刃の摩耗状況も正常であるのに対して、従来被覆超硬工具１〜４は、特に硬質被覆層を構成するＡｌＯＺ 層の高温での熱伝導性の低下が著しく、これが原因で刃先の摩耗進行が促進するようにな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、例えば鋼の通常の条件での連続切削および断続切削は勿論のこと、熱発生が高く、刃先の加熱が著しい高速切削でもすぐれた耐摩耗性を示し、長期に亘ってすぐれた切削性能を発揮するものである。
【図面の簡単な説明】
【図１】 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 exhibits high-temperature thermal conductivity with a hard coating layer excellent in cutting with particularly high heat generation. Therefore, even when used for, for example, high-speed cutting in which the cutting edge is exposed to high temperature, the progress of wear of the cutting edge is increased. The present invention relates to a cutting tool made of a surface-coated carbide material that is suppressed and exhibits excellent wear resistance over a long period of time (hereinafter referred to as a coated carbide tool).
[0002]
[Prior art]
Conventionally, for example, an arc ion plating apparatus which is one type of physical vapor deposition apparatus shown in a schematic explanatory diagram in FIG. 1 is used, and an anode electrode and metallic Ti or Arc discharge is generated between the cathode electrode (evaporation source) on which metal Al is set, and at the same time, as the reaction gas in the apparatus, when the metal Ti is set on the cathode electrode, methane gas, nitrogen gas, or Nitrogen gas and methane gas are introduced, and oxygen gas is introduced when the metal Al is set, while tungsten carbide (hereinafter referred to as WC) based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN). For a substrate made of a cermet (hereinafter collectively referred to as a carbide substrate), for example, under the condition that a bias voltage of −70 V is applied, On the surface of the substrate,
(A) All have an average layer thickness of 0.1 to 5 μm, and when expressed by the composition formulas: TiC E , TiN E , and Ti (C 1-F N F ) E , respectively, E : Ti compound layer composed of one or more of a titanium carbide layer, a titanium nitride layer, and a titanium carbonitride layer satisfying 0.8 to 1.2 and F : 0.3 to 0.7,
(B) having an average layer thickness of 0.1 to 10 μm, and
Composition formula: AlO Z ,
In this case, an aluminum oxide layer (hereinafter referred to as an AlO Z layer) satisfying Z : 1-2 in terms of atomic ratio,
An attempt has been made to produce a coated carbide tool formed by physical vapor deposition of the hard coating layer constituted by (a) and (b) with an overall average layer thickness of 0.5 to 20 μm, and for practical application. Research is underway.
[0003]
[Problems to be solved by the invention]
On the other hand, high performance and high output of cutting equipment in recent years are remarkable, and there are many demands for labor saving and energy saving of cutting work.Accordingly, cutting tends to be faster. In carbide tools, when this is used for high-speed cutting with high heat generation, the Ti compound layer constituting the hard coating layer exhibits excellent high-temperature thermal conductivity, but the AlO Z layer is exposed to high temperatures. If this happens, the thermal conductivity will drop sharply, so the temperature rise of the cutting edge will be unavoidable, and this will promote the progress of wear, and the service life will be reached in a relatively short time. .
[0004]
[Means for Solving the Problems]
Therefore, the present inventors, from the viewpoint as described above, as a result of conducting research to develop a coated carbide tool that exhibits excellent wear resistance in high heat generation cutting,
In place of the AlO Z layer constituting the hard coating layer of the above conventional coated carbide tool, zirconium oxide with excellent high-temperature thermal conductivity, that is, composition formula: ZrO Z (where Z is an atomic ratio of 1.5 to 2.5)), and a part of Zr thereof is selected from the group consisting of V, Cr, and Y (hereinafter referred to as M) for the purpose of improving high-temperature hardness. A hard coating layer made of a Zr-based composite oxide substituted with a Zr-based composite oxide, that is, a composition formula: (Zr 1-X M X ) O Z (where X: 0.01 to 0.3 in terms of atomic ratio, Z : 1. 5 to 2.5) is applied in a state where the hard coating layer is also coexisted with the Ti compound layer, the hard coating layer becomes the Zr composite oxide layer and Ti. The coated carbide tool composed of the compound layer is the Zr-based composite oxide layer. Due to the excellent high-temperature thermal conductivity of the Ti compound layer and the high-temperature hardness of the Zr-based composite oxide layer, it can be used for high-speed cutting such as steel with high heat generation. Research results have been obtained that the progress of wear of the blade is suppressed and the wear resistance is improved over a long period of time.
[0005]
This invention was made based on the above research results, and on the surface of the carbide substrate,
(A) All have an average layer thickness of 0.1 to 5 μm, and when expressed by the composition formulas: TiC E , TiN E , and Ti (C 1-F N F ) E , respectively, E : Ti compound layer composed of one or more of a titanium carbide layer, a titanium nitride layer, and a titanium carbonitride layer satisfying 0.8 to 1.2 and F : 0.3 to 0.7,
(B) Each average layer thickness is 0.1 to 10 μm, and
Composition formula: (Zr 1-X M X ) O Z ,
(However, M consists of one of V, Cr, and Y ),
A Zr-based composite oxide layer satisfying an atomic ratio of X: 0.01 to 0.3, Z : 1.5 to 2.5,
A coated carbide tool that exhibits excellent wear resistance in high heat generation cutting, which is obtained by physically vapor-depositing the hard coating layer composed of (a) and (b) with an overall average layer thickness of 0.5 to 20 μm. It has characteristics.
[0006]
Next, the reason why the composition formula and the average layer thickness of the Ti compound layer and the Zr-based composite oxide layer constituting the hard coating layer are limited as described above in the coated carbide tool of the present invention will be described.
(A) Ti compound layer The Ti compound layer has low toughness compared to the Zr-based composite oxide layer, which is the same constituent layer, but has high toughness, so that the hard coating layer has a predetermined toughness. It is indispensable for providing it, and by this, it exerts the action of suppressing the occurrence of chipping or chipping (minute chipping) in the cutting edge in practical use, and the relative hardness is also a titanium nitride layer, titanium carbonitride The layers become higher in the order of the titanium carbide layer and the titanium carbide layer, both of which have excellent high-temperature thermal conductivity equivalent to that of the Zr-based composite oxide layer. On the other hand, an average layer thickness of up to 5 μm is sufficient for the above action, and no further layer thickness is necessary, so the average layer thickness was determined to be 0.1 to 5 μm.
The E value in each Ti compound layer is too soft when the value is less than 0.8, and the wear resistance is remarkably reduced. On the other hand, when the value exceeds 1.2, the layer Since it becomes brittle and causes defects, the E value is set to 0.8 to 1.2.
Further, F value in the titanium carbonitride layer, since its value also becomes less than 0.3, can not be held intermediate characteristics titanium carbide layer and a titanium nitride layer even beyond 0.7, F value Is defined as 0.3 to 0.7.
[0007]
(B) Zr-based composite oxide layer The Zr-based composite oxide layer that also constitutes the hard coating layer has excellent high-temperature hardness due to the M component while maintaining the excellent high-temperature thermal conductivity of ZrO Z as described above. Therefore, it exhibits an effect of suppressing a decrease in wear resistance at the time of high heat generation cutting, but the X value indicating the ratio of the M component to the total amount of Zr in the composition formula is 0.01- When the X value is less than 0.01, a desired improvement effect cannot be obtained in the high-temperature hardness of the Zr-based composite oxide layer. On the other hand, when the X value exceeds 0.3, the toughness is particularly high. The reason is that the X value of 0.05 to 0.25 is desirable because it is abruptly lowered and defects such as chipping and chipping are likely to occur in the desired cutting edge.
The reason why the Z value in the Zr-based composite oxide layer is determined to be 1.5 to 2.5 in terms of atomic ratio is that when the Z value is less than 1.5, the ratio of oxygen to Zr is relatively small. This is based on the reason that the desired excellent high-temperature thermal conductivity cannot be ensured, and on the other hand, if the Z value exceeds 2.5, the layer itself suddenly becomes brittle, which causes the occurrence of defects.
Furthermore, the reason why the individual average layer thickness of the Zr-based composite oxide layer is set to 0.1 to 10 μm is that when the layer thickness is less than 0.1 μm, the desired excellent wear resistance cannot be ensured. On the other hand, if the layer thickness exceeds 10 μm, chipping is likely to occur at the cutting edge, and preferably 0.2 to 5.0 μm.
[0008]
Also, the overall average layer thickness of the hard coating layer is set to 0.5 to 20 μm because if the layer thickness is less than 0.5 μm, a desired effect cannot be obtained in improving the wear resistance by the hard coating layer, while the layer This is because when the thickness exceeds 20 μm, chipping is likely to occur at the cutting edge, and the average layer thickness is preferably 3 to 10 μm.
[0009]
DETAILED DESCRIPTION OF THE INVENTION
Next, the coated carbide tool of the present invention will be specifically described with reference to examples.
As raw material powders, WC powder, TiC powder, TaC powder, and Co powder each having an average particle diameter of 0.5 to 3.5 μm are prepared. These raw material powders are WC: 90% by weight, TiC: 1%, TaC: 1%, Co: 8% blended composition, wet-mixed for 72 hours with a ball mill, dried, and then pressed into a green compact with a pressure of 1.5 ton / cm 2. The powder was sintered in vacuum at a temperature of 1450 ° C. for 1 hour, and after sintering, the cutting edge part was subjected to a honing process of R: 0.03 to have an ISO standard / SEKN1203AFEN1 chip shape. A cemented carbide substrate A made of a WC-based cemented carbide was formed.
In addition, as raw material powders, TiCN having an average particle diameter of 0.5 to 2 μm [by weight, TiC / TiN = 50/50] powder, TaC powder, WC powder, VC powder, Co powder, Ni powder, And graphite (C) powder, and these raw material powders are, by weight, TiCN: 74.5%, TaC: 3%, WC: 9.5%, VC: 1%, Co: 8%, Ni: 3%, C: 1% blended composition, wet-mixed for 24 hours in a ball mill, dried, then pressed into a green compact at a pressure of 1 ton / cm 2 , and this green compact was in a 5 torr nitrogen atmosphere Medium: Sintered at 1500 ° C for 1 hour. After sintering, made by TiCN cermet with honing of R: 0.03 on the cutting edge part and ISO standard SEEN1203AFEN1 chip shape. Forming a carbide substrate B of It was.
[0010]
Next, these superhard substrates A and B were ultrasonically cleaned in acetone and dried, and then charged into the arc ion plating apparatus shown in FIG. 1, respectively, while various cathode electrodes (evaporation sources) were used. A Zr-M alloy having a component composition, metal Ti, and metal Al were mounted, and the inside of the apparatus was heated to 400 ° C. with a heater while evacuating the apparatus and maintaining a vacuum of 1 × 10 −5 torr. After that, when a bias voltage of −50 V is applied to the cemented carbide substrate and a Ti compound layer is formed with the cathode electrode as metal Ti as a reaction gas in the apparatus, methane gas, nitrogen gas, or nitrogen gas and methane gas are used. When the cathode electrode is a Zr-M alloy or metal Al to form a Zr-based composite oxide layer or an AlO Z layer, oxygen gas is introduced and the cathode is An arc discharge is generated between the cathode electrode and the anode electrode, so that a hard coating layer having a target composition and a target layer thickness shown in Tables 1 to 3 is physically vapor-deposited on each surface of the cemented carbide substrates A and B. The present invention coated carbide tools 1 to 7 in which the hard coating layer is composed of a Ti compound layer and a Zr-based composite oxide layer, and the conventional coating in which the hard coating layer is composed of a Ti compound layer and an AlO Z layer Carbide tools 1 to 4 were produced, respectively.
In addition, about the said various coated carbide tools, when the cross section of this hard coating layer was observed with the scanning electron microscope and the composition and layer thickness were measured, the target composition and target layer which are shown in Tables 1-3 It showed substantially the same composition and average layer thickness as the thickness.
[0011]
Among the various coated cemented carbide tools obtained as a result, the present coated cemented carbide tools 1 to 4 and the conventional coated cemented carbide tools 1 and 2,
Work material: Square material of JIS / SNCM439 (hardness: HR C30),
Cutting speed: 280 m / min,
Feed: 0.2mm / blade (single blade),
Incision: 1.5mm,
Cutting time: 25 minutes,
A dry high-speed milling test of alloy steel under the following conditions (referred to as cutting condition A), and work material: JIS SKD61 (hardness: HR C60) square material,
Cutting speed: 300 m / min,
Feed: 0.08mm / blade (single blade),
Cutting depth: 1mm,
Cutting time: 10 minutes,
The dry high-speed milling cutting test of the hardened steel under the above conditions (referred to as cutting condition B) was performed, and for the coated carbide tools 5 to 7 and the comparative coated carbide tools 3 and 4 of the present invention,
Work material: Square material of JIS / SNCM439 (hardness: HR C32),
Cutting speed: 350 m / min,
Feed: 0.15 mm / blade (single blade),
Incision: 1.5mm,
Cutting time: 20 minutes,
A dry high-speed milling cutting test of alloy steel under the following conditions (referred to as cutting condition C), and a work material: JIS SKD61 (hardness: HR C55) square material,
Cutting speed: 320 m / min,
Feed: 0.1 mm / blade (single blade),
Cutting depth: 1mm,
Cutting time: 15 minutes,
The dry high-speed milling cutting test was performed on the hardened steel under the above conditions (referred to as cutting condition D), and the flank wear width of the cutting edge was measured in any cutting test. The measurement results are shown in Tables 2 and 3 .
[0012]
[Table 1]
[Table 2]
[Table 3]
【The invention's effect】
From the results shown in Tables 1 to 3 , the coated carbide tools 1 to 7 of the present invention all have high-temperature thermal conductivity in which the Zr-based composite oxide layer and the Ti compound layer constituting the hard coating layer are excellent, In addition, the Zr-based composite oxide layer is excellent in high-temperature hardness, and the Ti compound layer is excellent in toughness, so that the hard coating layer can be used for high-speed cutting of high-hardness steel whose blade edge is heated at high temperature. Since the deterioration of the thermal conductivity of the blade is suppressed and overheating of the cutting edge is prevented, excellent wear resistance is exhibited and the cutting blade wear state is normal, whereas the conventional coated carbide tool 1 In No. 4, it is clear that the thermal conductivity at the high temperature of the AlO Z layer constituting the hard coating layer is particularly lowered, and this promotes the progress of wear of the blade edge.
As described above, the coated carbide tool of the present invention has excellent wear resistance even in high-speed cutting with high heat generation as well as continuous cutting and intermittent cutting under normal conditions of steel, for example. And exhibit excellent cutting performance over a long period of time.
[Brief description of the drawings]
FIG. 1 is a schematic explanatory diagram of an arc ion plating apparatus.
Claims (1)
（ａ）いずれも０．１〜５μｍの平均層厚を有し、かつそれぞれ組成式：ＴｉＣＥ 、ＴｉＮＥ 、およびＴｉ（Ｃ１−ＦＮＦ）Ｅ
で表した場合、原子比でＥ：０．８〜１．２、Ｆ：０．３〜０．７を満足する炭化チタン層、窒化チタン層、および炭窒化チタン層のうちの１層または２層以上からなるＴｉ化合物層、
（ｂ）それぞれ個々の平均層厚が０．１〜１０μｍにして、かつ、
組成式：（Ｚｒ１−Ｘ ＭＸ ）ＯＺ 、
（ただし、ＭはＶ、Ｃｒ、およびＹのうちの１種からなる）、
で表した場合、原子比でＸ：０．０１〜０．３、Ｚ：１．５〜２．５を満足するＺｒと上記Ｍ成分とのＺｒ系複合酸化物層、
以上（ａ）および（ｂ）で構成された硬質被覆層を０．５〜２０μｍの全体平均層厚で物理蒸着してなる、高熱発生切削ですぐれた耐摩耗性を発揮する表面被覆超硬材料製切削工具。On the surface of a tungsten carbide base cemented carbide substrate or a titanium carbonitride cermet substrate,
(A) All have an average layer thickness of 0.1 to 5 μm, and composition formulas: TiC E , TiN E , and Ti (C 1-F N F ) E
1 or 2 of the titanium carbide layer, the titanium nitride layer, and the titanium carbonitride layer satisfying E : 0.8 to 1.2 and F : 0.3 to 0.7 in the atomic ratio. Ti compound layer consisting of more than one layer,
(B) Each average layer thickness is 0.1 to 10 μm, and
Composition formula: (Zr 1-X M X ) O Z ,
(However, M consists of one of V, Cr, and Y ),
A Zr-based composite oxide layer of Zr and the above M component satisfying an atomic ratio of X: 0.01 to 0.3, Z : 1.5 to 2.5,
Surface-coated cemented carbide material that exhibits excellent wear resistance in high heat generation cutting, which is obtained by physically vapor-depositing the hard coating layer composed of (a) and (b) with an overall average layer thickness of 0.5 to 20 μm. Cutting tool made.
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| JP12795699A JP3899501B2 (en) | 1999-05-10 | 1999-05-10 | Cutting tool made of surface-coated carbide material that exhibits excellent wear resistance in high heat generation cutting |
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| JP3534091B2 (en) | 2001-07-12 | 2004-06-07 | 三菱マテリアル神戸ツールズ株式会社 | Surface-coated cemented carbide cutting tool with excellent surface lubricity to chips |
| CN109504868A (en) * | 2018-10-30 | 2019-03-22 | 湖南工业大学 | A kind of mine tool hard alloy and preparation method thereof |
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