JPH10225804A - Surface-coated cemented carbide cutting tool excellent in chipping resistance and manufacture therefor - Google Patents
Surface-coated cemented carbide cutting tool excellent in chipping resistance and manufacture thereforInfo
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- JPH10225804A JPH10225804A JP9026498A JP2649897A JPH10225804A JP H10225804 A JPH10225804 A JP H10225804A JP 9026498 A JP9026498 A JP 9026498A JP 2649897 A JP2649897 A JP 2649897A JP H10225804 A JPH10225804 A JP H10225804A
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- cutting edge
- vapor deposition
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、すぐれた耐欠損
性を有し、したがって特に耐欠損性が要求される、例え
ば鋼の断続重切削などに用いた場合にも切刃に欠損の発
生なく、すぐれた切削性能を長期に亘って発揮する表面
被覆超硬合金製切削工具（以下、被覆超硬工具と云
う）、およびその製造法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention has excellent fracture resistance, and therefore, is required to have particularly high fracture resistance. The present invention relates to a surface-coated cemented carbide cutting tool that exhibits excellent cutting performance over a long period of time (hereinafter referred to as a coated cemented carbide tool), and a method of manufacturing the same.
【０００２】[0002]
【従来の技術】従来、一般に被覆超硬工具が、図２の切
刃部縦断面を光学顕微鏡で観察した組織による概略工程
図で示される通り、（ａ） Ｃｏおよび／またはＮｉを
主成分とする結合相形成成分：５〜１５重量％、Ｔｉ、
Ｔａ、Ｎｂ、Ｚｒ、およびＨｆの窒化物および炭窒化物
（以下、それぞれＴｉＮ、ＴａＮ、ＮｂＮ、ＺｒＮ、お
よびＨｆＮ、さらにＴｉＣＮ、ＴａＣＮ、ＮｂＣＮ、Ｚ
ｒＣＮ、およびＨｆＣＮで示す）、並びにこれらの２種
以上の固溶体のうちの１種または２種以上からなるβ相
形成成分：１〜１０重量％を含有する炭化タングステン
基超硬合金（以下、単に超硬合金と云う）で構成され、
かつ表面部に、すくい面、すくい面と逃げ面の交わる切
刃稜線部、および逃げ面にかけて層厚が５〜３０μｍの
β相が存在しない、すなわち基体内部に比して硬さの低
い脱β相帯域が存在する基体を用意し、（ｂ） 上記基
体の切刃稜線部に、すくい面側からみた幅で０．０３〜
０．３ｍｍのホーニング加工を施して所定寸法とし、
（ｃ）上記ホーニング加工後の基体の全面に亘って、Ｔ
ｉの炭化物、窒化物、炭窒化物、炭酸化物、および炭窒
酸化物、さらに酸化アルミニウム（以下、それぞれＴｉ
Ｃ、ＴｉＮ、ＴｉＣＮ、ＴｉＣＯ、およびＴｉＣＮＯ、
さらにＡｌ2 Ｏ 3 で示す）のうちの１種の単層または２
種以上の複層からなる硬質被覆層を、同じく化学蒸着法
および／または物理蒸着法にて５〜２０μｍの平均層厚
で形成する、以上（ａ）〜（ｃ）の基本工程によって製
造され、またこの被覆超硬工具が、鋼や鋳鉄などの連続
切削や断続切削に用いられることも知られている。2. Description of the Related Art Conventionally, a coated carbide tool is generally used as a cutting tool shown in FIG.
Schematic process by microstructure of the blade section observed by optical microscope
As shown in the figure, (a) Co and / or Ni
Bonding phase forming component as a main component: 5 to 15% by weight, Ti,
Nitride and carbonitride of Ta, Nb, Zr, and Hf
(Hereinafter, TiN, TaN, NbN, ZrN,
And HfN, and also TiCN, TaCN, NbCN, Z
rCN, and HfCN), and two of these.
Β phase consisting of one or more of the above solid solutions
Forming component: Tungsten carbide containing 1 to 10% by weight
It is composed of base cemented carbide (hereinafter simply referred to as cemented carbide),
The rake face, the face where the rake face meets the flank face
The layer thickness is 5 to 30 μm over the ridgeline and flank.
Absence of β phase, that is, lower hardness than inside the substrate
A substrate having a β-phase zone is prepared, and (b)
0.03 to width of the cutting edge of the body as viewed from the rake face
0.3mm honing processing to give the specified dimensions,
(C) T over the entire surface of the substrate after honing
i carbides, nitrides, carbonitrides, carbonates, and carbonitrides
Oxide and aluminum oxide (hereinafter referred to as Ti
C, TiN, TiCN, TiCO, and TiCNO;
Further AlTwoO ThreeMonolayer or 2 of
Hard coating layer consisting of multiple layers
And / or 5-20 μm average layer thickness by physical vapor deposition
Formed by the above basic steps (a) to (c).
And the coated carbide tool is used for continuous machining of steel, cast iron, etc.
It is also known to be used for cutting and intermittent cutting.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の切削装置
のＦＡ化および高性能化はめざましく、かつ切削加工の
省力化および省エネ化に対する要求も強く、これに伴
い、切削加工は連続切削は勿論のこと、断続切削も可能
であるばかりでなく、高送りや高切り込みなどの重切削
にも適用できる切削工具が求められる傾向にあるが、上
記の従来被覆超硬工具においては、上記のホーニング加
工で切刃稜線部の脱β相帯域の厚さ方向の一部あるいは
全部が除去されるため、切刃稜線部の脱β相帯域の厚さ
はすくい面および逃げ面における脱β相帯域の厚さに比
して相対的に薄く、あるいはこれが皆無となるため、例
えばこれを鋼の断続重切削に用いた場合、特に切刃稜線
部に欠けが発生し易く、実用に供することができないの
が現状である。On the other hand, in recent years, the cutting equipment has been remarkably changed to FA and high performance, and there is also a strong demand for labor saving and energy saving of the cutting work. In addition, not only intermittent cutting is possible, but also cutting tools that can be applied to heavy cutting such as high feed and high cutting tend to be demanded. Because part or all in the thickness direction of the β-phase zone of the cutting edge is removed in the thickness direction, the thickness of the β-phase zone at the cutting edge is the thickness of the β-phase zone at the rake face and flank. Since it is relatively thin compared to that, or it is completely absent, for example, when it is used for intermittent heavy cutting of steel, chipping tends to occur especially at the cutting edge ridge line, and it can not be used practically It is the current situation.
【０００４】[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、上記の従来被覆超硬工具に着目
し、これの耐欠損性向上をはかるべく研究を行った結
果、被覆超硬工具を製造するに際して、図１の切刃部縦
断面を光学顕微鏡で観察した組織による概略工程図で示
される通り、Ｃｏおよび／またはＮｉを主成分とする結
合相形成成分：５〜１５重量％、ＴｉＮ、ＴａＮ、Ｎｂ
Ｎ、ＺｒＮ、およびＨｆＮ、さらにＴｉＣＮ、ＴａＣ
Ｎ、ＮｂＣＮ、ＺｒＣＮ、およびＨｆＣＮ、並びにこれ
らの２種以上の固溶体のうちの１種または２種以上から
なるβ相形成成分：１〜１０重量％を含有する超硬合金
で構成され、かつ表面部に、切刃部縦断面を光学顕微鏡
で観察した組織（以下、同じ）で、すくい面、切刃稜線
部、および逃げ面にかけて層厚が５〜３０μｍのβ相が
存在しない、基体内部に比して硬さの低い脱β相帯域が
存在する基体の表面に、あらかじめＴｉ、Ｚｒ、および
Ｈｆの炭化物および炭窒化物（以下、それぞれＴｉＣ、
ＺｒＣ、およびＨｆＣ、さらにＴｉＣＮ、ＺｒＣＮ、お
よびＨｆＣＮで示す）のうちの１種の単層または２種以
上の複層からなる硬質層を化学蒸着法および／または物
理蒸着法にて１〜５μｍの平均層厚で形成した状態で、
すくい面側からみた幅で０．０３〜０．３ｍｍのホーニ
ング加工を施し、このホーニング加工で切刃稜線部の上
記硬質層、および同じく切刃稜線部の脱β相帯域の厚さ
方向の一部あるいは全部が除去されるため、切刃稜線部
の脱β相帯域の厚さはすくい面および逃げ面における脱
β相帯域の厚さに比して相対的に薄く、あるいはこれが
皆無となるが、これを真空雰囲気中、１３５０〜１５０
０℃の温度に加熱すると、切刃稜線部の基体表面部にお
けるβ相が分解し、これの構成成分である窒素（Ｎ）成
分が真空雰囲気に放出され、これによって切刃稜線部の
基体表面部における脱β相帯域の厚さ方向の形成が進行
し、一方すくい面および逃げ面の表面部における脱β相
帯域のさらなる厚さ方向の形成（肉厚化）は、上記ホー
ニング加工で除去されずに残留した上記硬質層によって
Ｎ成分の真空雰囲気への放出が阻止されるために行われ
ないことから、前記加熱温度に所定時間保持することに
よって、基体表面部にはすくい面、切刃稜線部、および
逃げ面にかけて実質的に同じ厚さの脱β相帯域が形成さ
れるようになり、この状態で、上記の硬質被覆層を、同
じく化学蒸着法および／または物理蒸着法にて５〜２０
μｍの平均層厚で形成すると、製造された被覆超硬工具
は、基体表面部に実質的に同じ厚さで存在する脱β相帯
域によってすぐれた耐欠損性を示すようになるという研
究結果を得たのである。Means for Solving the Problems Accordingly, the present inventors have
In view of the above, the above-mentioned conventional coated carbide tools were focused on, and as a result of researching to improve the fracture resistance thereof, when manufacturing the coated carbide tools, the cutting edge longitudinal section of FIG. As shown in the schematic process drawing of the structure observed with an optical microscope, a binder phase forming component containing Co and / or Ni as a main component: 5 to 15% by weight, TiN, TaN, Nb
N, ZrN, and HfN, as well as TiCN, TaC
N, NbCN, ZrCN, and HfCN, and a β-phase-forming component composed of one or more of two or more of these solid solutions, composed of a cemented carbide containing 1 to 10% by weight and having a surface In the part, there is a β-phase with a layer thickness of 5 to 30 μm over the rake face, the cutting edge ridge part, and the flank, with a structure in which the longitudinal section of the cutting edge part is observed with an optical microscope (the same applies hereinafter). On the surface of the substrate where the de-beta phase zone having a relatively low hardness exists, carbides and carbonitrides of Ti, Zr, and Hf (hereinafter, TiC,
ZrC, and HfC, and also TiCN, ZrCN, and HfCN), and a hard layer composed of a single layer or a multilayer of two or more layers is formed by chemical vapor deposition and / or physical vapor deposition to a thickness of 1 to 5 μm. In the state formed with the average layer thickness,
Honing is performed with a width of 0.03 to 0.3 mm as viewed from the rake face side, and the honing is applied to the hard layer of the cutting edge ridge and the thickness direction of the β-phase removal zone of the cutting edge ridge. Since part or all is removed, the thickness of the β-phase zone at the cutting edge ridge portion is relatively thin compared to the thickness of the β-phase zone at the rake face and the flank, or there is no such zone. In a vacuum atmosphere, 1350-150
When heated to a temperature of 0 ° C., the β phase on the surface of the substrate at the cutting edge ridge is decomposed, and a nitrogen (N) component, which is a component thereof, is released into a vacuum atmosphere. The formation in the thickness direction of the de-β-phase zone in the portion proceeds, while the further formation of the β-phase zone in the thickness direction (thickening) at the rake face and the flank surface is removed by the honing process. Since the release of the N component into the vacuum atmosphere is prevented by the remaining hard layer without being removed, by keeping the heating temperature for a predetermined time, the rake face and the cutting edge ridge line are formed on the surface of the substrate. And the flank, a substantially equal thickness of the de-beta phase zone is formed, and in this state, the hard coating layer is formed by the chemical vapor deposition method and / or the physical vapor deposition method. 20
Research has shown that when formed at an average layer thickness of μm, the coated coated carbide tool produced exhibits excellent fracture resistance due to the de-beta phase zone present at substantially the same thickness on the substrate surface. I got it.
【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、（ａ） Ｃｏおよび／またはＮｉ
を主成分とする結合相形成成分：５〜１５重量％、Ｔｉ
Ｎ、ＴａＮ、ＮｂＮ、ＺｒＮ、およびＨｆＮ、さらにＴ
ｉＣＮ、ＴａＣＮ、ＮｂＣＮ、ＺｒＣＮ、およびＨｆＣ
Ｎ、並びにこれらの２種以上の固溶体のうちの１種また
は２種以上からなるβ相形成成分：１〜１０重量％を含
有する超硬合金、望ましくはＣｏおよび／またはＮｉを
主成分とする結合相形成成分：５〜１５重量％、Ｔｉ
Ｎ、ＴａＮ、ＮｂＮ、ＺｒＮ、およびＨｆＮ、さらにＴ
ｉＣＮ、ＴａＣＮ、ＮｂＣＮ、ＺｒＣＮ、およびＨｆＣ
Ｎ、並びにこれらの２種以上の固溶体のうちの１種また
は２種以上からなるβ相形成成分：１〜１０重量％を含
有し、残りが炭化タングステン（以下、ＷＣで示す）と
不可避不純物からなる組成を有する超硬合金で構成さ
れ、かつ表面部に、すくい面、すくい面と逃げ面の交わ
る切刃稜線部、および逃げ面にかけて層厚が５〜３０μ
ｍのβ相が存在しない、基体内部に比して硬さの低い脱
β相帯域が存在する基体を用意し、（ｂ） 上記基体の
表面に、ＴｉＣ、ＺｒＣ、およびＨｆＣ、さらにＴｉＣ
Ｎ、ＺｒＣＮ、およびＨｆＣＮのうちの１種の単層また
は２種以上の複層からなる脱β相帯域の成長抑止硬質層
を化学蒸着法および／または物理蒸着法にて１〜５μｍ
の平均層厚で形成し、（ｃ） 上記成長抑止硬質層形成
の基体の切刃稜線部にホーニング加工（通常、すくい面
側からみた幅で０．０３〜０．３ｍｍ）を施して所定寸
法とし、（ｄ） 上記ホーニング加工によって切刃稜線
部の成長抑止硬質層および脱β相帯域の厚さ方向の少く
とも一部が除去された基体に、真空中、１３５０〜１５
００℃の温度に加熱の熱処理を施して、真空雰囲気に直
接さらされる切刃稜線部での基体から真空雰囲気への脱
窒を行って切刃稜線部だけの脱β相帯域の厚さ方向の形
成をはかることにより、基体表面部にすくい面、切刃稜
線部、および逃げ面にかけて実質的に同じ厚さにして、
平均層厚が５〜３０μｍの脱β相帯域を形成し、（ｅ）
上記熱処理後の基体の全面に亘って、ＴｉＣ、Ｔｉ
Ｎ、ＴｉＣＮ、ＴｉＣＯ、およびＴｉＣＮＯ、さらにＡ
ｌ2 Ｏ3 のうちの１種の単層または２種以上の複層から
なる硬質被覆層を、同じく化学蒸着法および／または物
理蒸着法にて５〜２０μｍの平均層厚で形成する、以上
（ａ）〜（ｅ）の基本工程によって被覆超硬工具を製造
する方法、並びに、上記方法によって製造された、
（ａ） Ｃｏおよび／またはＮｉを主成分とする結合相
形成成分：５〜１５重量％、ＴｉＮ、ＴａＮ、ＮｂＮ、
ＺｒＮ、およびＨｆＮ、さらにＴｉＣＮ、ＴａＣＮ、Ｎ
ｂＣＮ、ＺｒＣＮ、およびＨｆＣＮ、並びにこれらの２
種以上の固溶体のうちの１種または２種以上からなるβ
相形成成分：１〜１０重量％を含有する超硬合金、望ま
しくはＣｏおよび／またはＮｉを主成分とする結合相形
成成分：５〜１５重量％、ＴｉＮ、ＴａＮ、ＮｂＮ、Ｚ
ｒＮ、およびＨｆＮ、さらにＴｉＣＮ、ＴａＣＮ、Ｎｂ
ＣＮ、ＺｒＣＮ、およびＨｆＣＮ、並びにこれらの２種
以上の固溶体のうちの１種または２種以上からなるβ相
形成成分：１〜１０重量％を含有し、残りがＷＣと不可
避不純物からなる組成を有する超硬合金で構成された基
体の表面部に、すくい面、切刃稜線部、および逃げ面に
かけて実質的に同じ厚さにして、平均層厚が５〜３０μ
ｍのβ相が存在しない、基体内部に比して硬さの低い脱
β相帯域が存在し、（ｂ） また、基体表面上の切刃稜
線部を除くすくい面と逃げ面には、化学蒸着法および／
または物理蒸着法にて１〜５μｍの平均層厚で形成され
た、ＴｉＣ、ＺｒＣ、およびＨｆＣ、さらにＴｉＣＮ、
ＺｒＣＮ、およびＨｆＣＮのうちの１種の単層または２
種以上の複層からなる脱β相帯域の成長抑止硬質層が存
在し、（ｃ） さらに、成長抑止硬質層および基体切刃
稜線部の全面に亘って、同じく化学蒸着法および／また
は物理蒸着法にて形成された、ＴｉＣ、ＴｉＮ、ＴｉＣ
Ｎ、ＴｉＣＯ、およびＴｉＣＮＯ、さらにＡｌ2 Ｏ3 の
うちの１種の単層または２種以上の複層からなる硬質被
覆層が５〜２０μｍの平均層厚で存在する断面構造をも
った被覆超硬工具、に特徴を有するものである。The present invention has been made on the basis of the above research results, and (a) Co and / or Ni
Phase forming component mainly composed of: 5 to 15% by weight, Ti
N, TaN, NbN, ZrN, and HfN, plus T
iCN, TaCN, NbCN, ZrCN, and HfC
N, and a β-phase forming component composed of one or more of these two or more solid solutions: a cemented carbide containing 1 to 10% by weight, preferably Co and / or Ni as a main component Bound phase forming component: 5 to 15% by weight, Ti
N, TaN, NbN, ZrN, and HfN, plus T
iCN, TaCN, NbCN, ZrCN, and HfC
N and one or more of these two or more solid solutions, β-phase-forming component: 1 to 10% by weight, the balance being tungsten carbide (hereinafter, referred to as WC) and unavoidable impurities. And a layer thickness of 5 to 30 μm over the rake face, the cutting edge ridge line where the rake face and the flank face intersect, and the flank face.
A substrate in which there is no β phase of m and a de-β phase zone having a lower hardness than the inside of the substrate is prepared. (b) TiC, ZrC, HfC, and TiC are formed on the surface of the substrate.
A single layer of one of N, ZrCN, and HfCN or a growth-suppressing hard layer composed of a multilayer of two or more layers in a β-phase removal zone is formed to a thickness of 1 to 5 μm by a chemical vapor deposition method and / or a physical vapor deposition method.
(C) Honing (usually 0.03 to 0.3 mm in width as viewed from the rake face side) on the cutting edge ridge of the substrate on which the above-described growth-inhibiting hard layer is formed, (D) The substrate from which at least a part of the growth-inhibiting hard layer at the edge of the cutting edge and the at least part of the β-removed phase zone in the thickness direction has been removed by the honing process, is subjected to a vacuum at 1350 to 15
A heat treatment of heating to a temperature of 00 ° C. is performed, and the denitrification from the substrate to the vacuum atmosphere is performed at the cutting edge ridge portion directly exposed to the vacuum atmosphere. By measuring the formation, the rake surface on the substrate surface, the cutting edge ridge portion, and the flank surface to have substantially the same thickness,
(E) forming a de-β-phase zone having an average layer thickness of 5 to 30 μm;
TiC, Ti over the entire surface of the substrate after the heat treatment
N, TiCN, TiCO, and TiCNO, plus A
A hard coating layer composed of one kind of single layer or two or more kinds of l 2 O 3 is similarly formed with an average layer thickness of 5 to 20 μm by a chemical vapor deposition method and / or a physical vapor deposition method. (A) a method for producing a coated carbide tool by the basic steps of (e), and
(A) A binder phase forming component containing Co and / or Ni as a main component: 5 to 15% by weight, TiN, TaN, NbN,
ZrN and HfN, as well as TiCN, TaCN, N
bCN, ZrCN, and HfCN, and their 2
Β consisting of one or more of the solid solutions
Phase forming component: cemented carbide containing 1 to 10% by weight, desirably a binder phase forming component containing Co and / or Ni as a main component: 5 to 15% by weight, TiN, TaN, NbN, Z
rN and HfN, as well as TiCN, TaCN, Nb
CN, ZrCN, and HfCN, and a β-phase forming component consisting of one or more of two or more of these solid solutions: 1 to 10% by weight, and the balance being WC and unavoidable impurities. The surface portion of the substrate made of cemented carbide having the rake face, the cutting edge ridge portion, and the flank face have substantially the same thickness, and the average layer thickness is 5 to 30 μm.
There is a β-phase zone having a lower hardness than the inside of the substrate, in which there is no β phase of m, and (b) a rake face and a flank except for a cutting edge ridge on the surface of the substrate have chemical Evaporation method and / or
Alternatively, TiC, ZrC, and HfC formed with an average layer thickness of 1 to 5 μm by physical vapor deposition, and TiCN,
ZrCN, and one monolayer or 2 of HfCN
There is a hard layer for inhibiting the growth of the β-removed phase zone composed of a plurality of layers of at least one kind. , TiN, TiC formed by the method
N, TiCO, TiCNO, and a coating superstructure having a cross-sectional structure in which a hard coating layer composed of a single layer or two or more layers of Al 2 O 3 is present with an average layer thickness of 5 to 20 μm. A hard tool.
【０００６】つぎに、この発明の被覆超硬工具、および
その製造法において、基体の組成、脱β相帯域、脱β相
帯域の成長抑止硬質層、および硬質被覆層の平均層厚、
さらに熱処理温度を上記の通りに数値限定した理由を説
明する。Next, in the coated cemented carbide tool of the present invention and the method of manufacturing the same, the composition of the substrate, the β-free zone, the growth-suppressing hard layer in the β-free zone, and the average thickness of the hard coating layer,
Further, the reason why the heat treatment temperature is numerically limited as described above will be described.
【０００７】（１） 基体の結合相形成成分の含有量 結合相形成成分には、焼結性を促進し、もって基体の強
度を向上させる作用があるが、その含有量が５重量％未
満では前記作用に所望の効果が得られず、一方その含有
量が１５重量％を越えると、耐摩耗性が急激に低下する
ようになることから、その含有量を５〜１５重量％と定
めた。(1) Content of Boundary Phase Forming Component of Substrate The binding phase forming component has an effect of promoting sintering properties and thus improving the strength of the substrate. If the desired effect cannot be obtained in the above-mentioned operation, and if the content exceeds 15% by weight, the abrasion resistance rapidly decreases, so the content is set to 5 to 15% by weight.
【０００８】（２） 基体のβ相形成成分の含有量 β相形成成分には、基体の硬さを向上させて耐摩耗性を
向上させる作用があるが、その含有量が１重量％未満で
は前記作用に所望の効果が得られず、一方その含有量が
１０重量％を越えると、耐欠損性が低下するようになる
ことから、その含有量を１〜１０重量％と定めた。(2) Content of β-phase-forming component of substrate The β-phase-forming component has the effect of improving the hardness of the substrate and improving the wear resistance. However, if the content is less than 1% by weight, If the desired effect cannot be obtained in the above operation, and if the content exceeds 10% by weight, the fracture resistance decreases, so the content is set to 1 to 10% by weight.
【０００９】（３） 基体表面部の脱β相帯域の平均層
厚 上記の通り脱β相帯域には、実質的にβ相が存在せず、
これによって基体内部に比して相対的に低い硬さを有す
るようになり、耐欠損性を向上させる作用があるが、そ
の平均層厚が５μｍ未満では、所望の耐欠損性を確保す
ることができず、一方その平均層厚が３０μｍを越える
と、基体に塑性変形が発生し易くなり、この結果切刃が
偏摩耗して短時間で使用寿命に至るようになることか
ら、その平均層厚を５〜３０μｍと定めた。(3) Average layer thickness of de-β-phase zone on substrate surface As described above, β-phase does not substantially exist in the de-β-phase zone.
As a result, the material has a relatively low hardness as compared with the inside of the base, and has an effect of improving the fracture resistance. However, if the average layer thickness is less than 5 μm, the desired fracture resistance can be secured. On the other hand, if the average layer thickness exceeds 30 μm, plastic deformation is likely to occur in the base, resulting in uneven wear of the cutting edge and a short service life. Was determined to be 5 to 30 μm.
【００１０】（４） 成長抑止硬質層の平均層厚 その平均層厚が１μｍ未満では、基体表面部のすくい面
と逃げ面における脱β相帯域の成長抑止に所望の効果が
得られず、一方前記の脱β相帯域の成長抑止効果は５μ
ｍまでの平均層厚で十分であることから、その平均層厚
を１〜５μｍと定めた。(4) Average Layer Thickness of the Growth Inhibiting Hard Layer If the average layer thickness is less than 1 μm, the desired effect cannot be obtained in suppressing the growth of the β-free zone at the rake face and flank face of the substrate surface. The growth suppression effect of the above-mentioned de-β-phase zone is 5 μm.
Since an average layer thickness up to m is sufficient, the average layer thickness was determined to be 1 to 5 μm.
【００１１】（５） 硬質被覆層の平均層厚 その平均層厚が５μｍ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、一方その平均層厚が２０μ
ｍを越えると、耐欠損性が低下し、切刃に欠損やチッピ
ング（微小欠け）などが発生し易くなることから、その
平均層厚を５〜２０μｍと定めた。(5) Average Layer Thickness of Hard Coating Layer If the average layer thickness is less than 5 μm, the desired excellent abrasion resistance cannot be secured, while the average layer thickness is 20 μm.
If it exceeds m, the chipping resistance is reduced, and chipping (chip chipping) or the like is likely to occur on the cutting edge. Therefore, the average layer thickness is set to 5 to 20 μm.
【００１２】（６） 熱処理温度 その温度が１３５０℃未満では、切刃稜線部における脱
β相帯域の形成が遅く、実用的でなく、一方その温度が
１５００℃を越えると、基体が軟化し、短命化の原因と
なる変形を起し易くなることから、その温度を１３５０
〜１５００℃と定めた。(6) Heat treatment temperature If the temperature is lower than 1350 ° C., the formation of the β-phase zone at the edge of the cutting edge is slow and impractical. On the other hand, if the temperature exceeds 1500 ° C., the substrate softens, Since the deformation that causes a short life is likely to occur, the temperature is set to 1350.
℃ 1500 ° C.
【００１３】[0013]
【発明の実施の形態】つぎに、この発明を実施例により
具体的に説明する。原料粉末として、いずれも１〜３μ
ｍの範囲内の平均粒径を有するＴｉＣ粉末、ＴａＣ粉
末、ＺｒＣ粉末、ＨｆＣ粉末、ＴｉＮ粉末、ＺｒＮ粉
末、ＴｉＣＮ粉末、（Ｔｉ，Ｗ）Ｃ（重量比で、以下同
じ、ＴｉＣ／ＷＣ＝３０／７０）粉末、（Ｔａ，Ｎｂ）
Ｃ（ＴａＣ／ＮｂＣ＝９０／１０）粉末、（Ｔｉ，Ｗ）
ＣＮ（ＴｉＣ／ＴｉＮ／ＷＣ＝２４／２０／５６）粉
末、Ｃｏ粉末、Ｎｉ粉末、ＶＣ粉末、およびＣｒ3 Ｃ2
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、所定形状の圧粉体にプレス成形し、この圧粉体を
０．０５ｔｏｒｒの真空中、１３８０〜１４５０℃の範
囲内の所定温度に１時間保持の条件で真空焼結すること
によりＩＳＯ規格１２０４０８のスローアウエイチップ
形状をもった超硬合金基体Ａ〜Ｆをそれぞれ製造した。
上記基体Ａ〜Ｆの切刃部縦断面の光学顕微鏡写真にもと
づき（以下同じ）、基体表面部の脱β相帯域の平均層厚
を測定したところ、表１に示される結果を示した。Next, the present invention will be specifically described with reference to examples. As raw material powder, each is 1-3μ
m, a TiC powder, a TaC powder, a ZrC powder, a HfC powder, a TiN powder, a ZrN powder, a TiCN powder, and a (Ti, W) C (TiC / WC = 30 by weight ratio) / 70) Powder, (Ta, Nb)
C (TaC / NbC = 90/10) powder, (Ti, W)
CN (TiC / TiN / WC = 24/20/56) powder, Co powder, Ni powder, VC powder, and Cr 3 C 2
Powders are prepared, and these raw material powders are blended in the composition shown in Table 1, wet-mixed in a ball mill for 72 hours, dried, and then pressed into a green compact having a predetermined shape. Cemented carbide substrates A to F having a throw-away chip shape according to ISO standard 120408 were manufactured by vacuum sintering at a predetermined temperature in the range of 1380 to 1450 ° C. for 1 hour in a vacuum of 05 torr. .
The average layer thickness of the β-phase-free zone on the surface of the substrate was measured based on the optical micrographs of the longitudinal sections of the cutting edges of the substrates A to F (the same applies hereinafter). The results shown in Table 1 were obtained.
【００１４】つぎに、上記基体Ａ〜Ｆの表面に、化学蒸
着法を用い、通常の条件で、それぞれ表２に示される組
成および平均層厚の脱β相帯域の成長抑止硬質層を形成
した後、同じく表２に示される加工量のホーニング加工
を施し、この時点で基体表面部の脱β相帯域の平均層厚
を測定したところ表２に示される結果を示し、ついで、
０．０１〜０．１ｔｏｒｒの範囲内の所定の圧力の真空
中、１３７０〜１４７０℃の範囲内の所定の温度に０．
５〜２時間の範囲内の所定の時間保持の条件で熱処理を
施し、同様にこの時点でも基体表面部の脱β相帯域の平
均層厚を測定したところ表３に示される結果を示し、さ
らに、同じく化学蒸着法を用い、通常の条件で、それぞ
れ表３に示される組成および平均層厚の硬質被覆層を形
成することからなる本発明法１〜１２を実施し、本発明
被覆超硬工具１〜１２をそれぞれ製造した。また、比較
の目的で、表５、６に示される通り、脱β相帯域の成長
抑止硬質層の形成、および脱β相帯域形成のための熱処
理を行わない以外は同一の条件で従来法１〜１２を行
い、従来被覆超硬工具１〜１２をそれぞれ製造した。Next, on the surfaces of the substrates A to F, a chemical vapor deposition method was used to form a growth-inhibiting hard layer having a composition and an average layer thickness shown in Table 2 in the de-beta phase zone under normal conditions. Thereafter, the same amount of honing as shown in Table 2 was performed, and at this time, the average layer thickness of the de-β-phase zone on the substrate surface was measured. The result shown in Table 2 was shown.
In a vacuum at a predetermined pressure in a range of 0.01 to 0.1 torr, a predetermined temperature in a range of 1370 to 1470 ° C. is set to 0.
Heat treatment was performed under the condition of holding for a predetermined time within the range of 5 to 2 hours. Similarly, at this time, the average layer thickness of the de-β-phase zone on the surface of the substrate was measured, and the results shown in Table 3 were obtained. In the same manner, using the chemical vapor deposition method, under normal conditions, the present invention methods 1 to 12 comprising forming a hard coating layer having the composition and the average layer thickness shown in Table 3, respectively, were carried out. 1 to 12 were produced respectively. Further, for comparison purposes, as shown in Tables 5 and 6, the conventional method 1 was used under the same conditions except that the formation of the hard layer for suppressing the growth of the β-free zone and the heat treatment for the formation of the β-free zone were not performed. To 12 were performed to produce conventional coated carbide tools 1 to 12, respectively.
【００１５】この結果得られた各種の被覆超硬工具につ
いて、 被削材：ＳＣＭ４３９（硬さ：Ｈｂ２３０）の角材、 切削速度：１００ｍ／ｍｉｎ、 送り：０．３７５ｍｍ／ｒｅｖ、 切り込み：３ｍｍ、 切削時間：１０分、 の条件で鋼の乾式高送り断続切削試験をおこない、切刃
の逃げ面摩耗幅を測定した。この測定結果を表６に示し
た。Worked material: square material of SCM439 (hardness: Hb230), cutting speed: 100 m / min, feed: 0.375 mm / rev, cutting depth: 3 mm, cutting A dry high-feed intermittent cutting test of steel was performed under the following conditions: 10 minutes, and the flank wear width of the cutting edge was measured. Table 6 shows the measurement results.
【００１６】[0016]
【表１】 [Table 1]
【００１７】[0017]
【表２】 [Table 2]
【００１８】[0018]
【表３】 [Table 3]
【００１９】[0019]
【表４】 [Table 4]
【００２０】[0020]
【表５】 [Table 5]
【００２１】[0021]
【表６】 [Table 6]
【００２２】[0022]
【発明の効果】表２〜６に示される通り、本発明法１〜
１２で製造された本発明被覆超硬工具１〜１２は、いず
れも基体表面部に、すくい面、切刃稜線部、および逃げ
面にかけて実質的に同じ厚さの脱β相帯域が存在し、こ
れによって鋼の高送り断続切削でも切刃に欠損の発生な
く、すぐれた耐摩耗性を示すのに対して、従来法１〜１
２で製造された従来被覆超硬工具１〜１２においては、
特に基体表面部の切刃稜線部に脱β相帯域が存在せず、
これが原因で上記の苛酷な条件での切削では切刃に欠損
の発生が避けられず、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、この発明の方法によ
れば、すぐれた耐摩耗性を保持した状態で、耐欠損性の
すぐれた被覆超硬工具を製造することができ、したがっ
てこの結果得られた被覆超硬工具は、通常の条件での連
続切削および断続切削は勿論のこと、一段と苛酷な条件
での切削となる断続切削を重切削で行っても切刃に欠損
の発生なく、すぐれた切削性能を長期に亘って発揮する
のである。As shown in Tables 2 to 6, the methods 1 to 5 of the present invention are shown.
Each of the coated carbide tools 1 to 12 of the present invention manufactured in No. 12 has a rake surface, a cutting edge ridge portion, and a β-phase zone having substantially the same thickness over the flank on the surface of the substrate, As a result, the cutting edge is not broken even at high feed interrupted cutting of steel and shows excellent wear resistance.
In the conventional coated carbide tools 1 to 12 manufactured in 2,
In particular, there is no β-phase zone at the cutting edge ridge on the surface of the base,
For this reason, it is apparent that in the cutting under the above-mentioned severe conditions, the occurrence of chipping of the cutting edge is inevitable, and the service life is relatively short. As described above, according to the method of the present invention, it is possible to produce a coated carbide tool having excellent fracture resistance while maintaining excellent wear resistance. The tool is capable of continuous cutting and intermittent cutting under normal conditions, as well as heavy cutting for intermittent cutting, which is cutting under more severe conditions. It is exerted over.
【図１】本発明方法を示す概略工程図である。FIG. 1 is a schematic process drawing showing the method of the present invention.
【図２】従来方法を示す概略工程図である。FIG. 2 is a schematic process diagram showing a conventional method.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｃ２３Ｃ 16/30 Ｃ２３Ｃ 16/30 ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 6 Identification code FI C23C 16/30 C23C 16/30
Claims (2)
結合相形成成分：５〜１５重量％、Ｔｉ、Ｔａ、Ｎｂ、
Ｚｒ、およびＨｆの窒化物および炭窒化物、並びにこれ
らの２種以上の固溶体のうちの１種または２種以上から
なるβ相形成成分：１〜１０重量％を含有する炭化タン
グステン基超硬合金で構成された基体の表面部に、切刃
部縦断面を光学顕微鏡で観察した組織で、すくい面、す
くい面と逃げ面の交わる切刃稜線部、および逃げ面にか
けて実質的に同じ厚さにして、平均層厚が５〜３０μｍ
のβ相が存在しない脱β相帯域が存在し、 また、基体表面上の切刃稜線部を除くすくい面と逃げ面
には、化学蒸着法および／または物理蒸着法にて１〜５
μｍの平均層厚で形成された、Ｔｉ、Ｚｒ、およびＨｆ
の炭化物および炭窒化物のうちの１種の単層または２種
以上の複層からなる脱β相帯域の成長抑止硬質層が存在
し、 さらに、成長抑止硬質層および基体切刃稜線部の全面に
亘って、同じく化学蒸着法および／または物理蒸着法に
て形成された、Ｔｉの炭化物、窒化物、炭窒化物、炭酸
化物、および炭窒酸化物、さらに酸化アルミニウムのう
ちの１種の単層または２種以上の複層からなる硬質被覆
層が５〜２０μｍの平均層厚で存在する表面被覆超硬合
金で構成したことを特徴とする耐欠損性のすぐれた表面
被覆超硬合金製切削工具。1. A binder phase forming component containing Co and / or Ni as a main component: 5 to 15% by weight, Ti, Ta, Nb,
Nitride and carbonitride of Zr and Hf, and a β-phase forming component consisting of one or more of two or more of these solid solutions: a tungsten carbide-based cemented carbide containing 1 to 10% by weight On the surface of the base body composed of, the rake face, the cutting edge ridge line where the rake face and the flank intersect, and the flank have substantially the same thickness, And the average layer thickness is 5 to 30 μm
And a rake face and a flank except for a cutting edge on the surface of the base are 1 to 5 by chemical vapor deposition and / or physical vapor deposition.
Ti, Zr, and Hf formed with an average layer thickness of μm
A single layer of at least one of carbides and carbonitrides of the above, and a growth-inhibiting hard layer in the de-β-phase zone comprising a multilayer of two or more types. Over one another, also formed by a chemical vapor deposition method and / or a physical vapor deposition method, comprising a carbide, a nitride, a carbonitride, a carbonate and a carbonitride of Ti, and one of aluminum oxide. Characterized in that the hard coating layer composed of one or more layers is composed of a surface-coated cemented carbide having an average layer thickness of 5 to 20 μm, and the surface-coated cemented carbide cutting having excellent fracture resistance. tool.
分とする結合相形成成分：５〜１５重量％、Ｔｉ、Ｔ
ａ、Ｎｂ、Ｚｒ、およびＨｆの窒化物および炭窒化物、
並びにこれらの２種以上の固溶体のうちの１種または２
種以上からなるβ相形成成分：１〜１０重量％を含有す
る炭化タングステン基超硬合金で構成され、かつ表面部
に、切刃部縦断面を光学顕微鏡で観察した組織で、すく
い面、すくい面と逃げ面の交わる切刃稜線部、および逃
げ面にかけて層厚が５〜３０μｍのβ相が存在しない脱
β相帯域が存在する基体を用意し、 （ｂ） 上記基体の表面に、Ｔｉ、Ｚｒ、およびＨｆの
炭化物および炭窒化物のうちの１種の単層または２種以
上の複層からなる脱β相帯域の成長抑止硬質層を化学蒸
着法および／または物理蒸着法にて１〜５μｍの平均層
厚で形成し、（ｃ） 上記成長抑止硬質層形成の基体の
切刃稜線部にホーニング加工を施し て所定寸法とし、 （ｄ） 上記ホーニング加工によって切刃稜線部の成長
抑止硬質層および脱β相帯域の少くとも一部が除去され
た基体に、真空中、１３５０〜１５００℃の温度に加熱
の熱処理を施して、真空雰囲気に直接さらされる切刃稜
線部での基体から真空雰囲気への脱窒を行って切刃稜線
部だけの脱β相帯域の厚さ方向の形成をはかることによ
り、基体表面部にすくい面、切刃稜線部、および逃げ面
にかけて実質的に同じ厚さにして、平均層厚が５〜３０
μｍの脱β相帯域を形成し、 （ｅ） 上記熱処理後の基体の全面に亘って、Ｔｉの炭
化物、窒化物、炭窒化物、炭酸化物、および炭窒酸化
物、さらに酸化アルミニウムのうちの１種の単層または
２種以上の複層からなる硬質被覆層を、同じく化学蒸着
法および／または物理蒸着法にて５〜２０μｍの平均層
厚で形成する、以上（ａ）〜（ｅ）の基本工程からなる
ことを特徴とする耐欠損性のすぐれた表面被覆超硬合金
製切削工具の製造法。2. (a) A bonding phase forming component containing Co and / or Ni as a main component: 5 to 15% by weight, Ti, T
nitrides and carbonitrides of a, Nb, Zr, and Hf;
And one or two of these two or more solid solutions
Β-phase forming component composed of at least one species: a tungsten carbide-based cemented carbide containing 1 to 10% by weight, and a rake face and a rake on its surface with a structure obtained by observing a longitudinal section of a cutting edge with an optical microscope. A substrate having a cutting edge ridge line where the surface and the flank intersect, and a β-phase free zone having a layer thickness of 5 to 30 μm over the flank where there is no β-phase; (b) Ti, The growth-inhibiting hard layer in the β-phase removal zone composed of one kind of single layer or two or more kinds of carbides and carbonitrides of Zr and Hf is formed by chemical vapor deposition and / or physical vapor deposition. (C) Honing is applied to the cutting edge ridge of the substrate on which the above-mentioned growth-inhibiting hard layer is formed to a predetermined size, and (d) The growth inhibiting hard of the cutting edge ridge is formed by the above-mentioned honing. Layer and at least part of the de-beta phase zone The removed substrate is subjected to a heat treatment of heating to a temperature of 1350 to 1500 ° C. in a vacuum, and denitrification from the substrate to the vacuum atmosphere is performed at the cutting edge ridge portion directly exposed to the vacuum atmosphere, thereby performing the cutting edge ridge portion. Only the thickness of the de-β-phase zone is measured in the thickness direction, so that the rake face, the cutting edge ridge, and the flank face are substantially the same thickness on the substrate surface portion, and the average layer thickness is 5 to 30.
(e) Ti carbides, nitrides, carbonitrides, carbonates, carbonitrides, and aluminum oxides are formed over the entire surface of the substrate after the heat treatment. A hard coating layer composed of one kind of single layer or two or more kinds of multiple layers is similarly formed by chemical vapor deposition and / or physical vapor deposition with an average layer thickness of 5 to 20 μm. A method for producing a surface-coated cemented carbide cutting tool with excellent fracture resistance, comprising the basic steps of (1).
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9026498A JPH10225804A (en) | 1997-02-10 | 1997-02-10 | Surface-coated cemented carbide cutting tool excellent in chipping resistance and manufacture therefor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9026498A JPH10225804A (en) | 1997-02-10 | 1997-02-10 | Surface-coated cemented carbide cutting tool excellent in chipping resistance and manufacture therefor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH10225804A true JPH10225804A (en) | 1998-08-25 |
Family
ID=12195163
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9026498A Withdrawn JPH10225804A (en) | 1997-02-10 | 1997-02-10 | Surface-coated cemented carbide cutting tool excellent in chipping resistance and manufacture therefor |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH10225804A (en) |
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| US6872234B2 (en) * | 1999-12-24 | 2005-03-29 | Kyocera Corporation | Cutting member |
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1997
- 1997-02-10 JP JP9026498A patent/JPH10225804A/en not_active Withdrawn
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| US7018726B2 (en) | 2001-09-26 | 2006-03-28 | Kyocera Corporation | Cemented carbide and cutting tool |
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| JP5221951B2 (en) * | 2005-03-28 | 2013-06-26 | 京セラ株式会社 | Cemented carbide and cutting tools |
| KR100996838B1 (en) | 2005-03-28 | 2010-11-26 | 쿄세라 코포레이션 | Super hard alloy and cutting tool |
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| JP2015182154A (en) * | 2014-03-20 | 2015-10-22 | 三菱マテリアル株式会社 | Surface-coated cutting tool having superior chipping resistance |
| CN106604796A (en) * | 2014-09-03 | 2017-04-26 | 三菱综合材料株式会社 | Surface-coated cutting tool and manufacturing method thereof |
| US10358712B2 (en) | 2014-09-03 | 2019-07-23 | Mitsubishi Materials Corporation | Surface-coated cutting tool and method of manufacturing the same |
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| A300 | Withdrawal of application because of no request for examination |
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