JPH1142504A - Surface coat tungesten carbide radical cemented carbide cutting tool excellent in heat resisting plastic deformability - Google Patents
Surface coat tungesten carbide radical cemented carbide cutting tool excellent in heat resisting plastic deformabilityInfo
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- JPH1142504A JPH1142504A JP20310997A JP20310997A JPH1142504A JP H1142504 A JPH1142504 A JP H1142504A JP 20310997 A JP20310997 A JP 20310997A JP 20310997 A JP20310997 A JP 20310997A JP H1142504 A JPH1142504 A JP H1142504A
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- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、すぐれた耐熱塑
性変形性を有し、かつ耐欠損性にもすぐれているので、
特に高い発熱量を伴う、例えば鋼や鋳鉄などの断続切削
を高速で行った場合にも、切刃に偏摩耗や、欠けおよび
チッピング（微小欠け）などの発生なく、すぐれた切削
性能を長期に亘って発揮する表面被覆炭化タングステン
基超硬合金製切削工具（以下、被覆超硬工具と云う）に
関するものである。TECHNICAL FIELD The present invention has excellent heat-resistant plastic deformation properties and excellent fracture resistance.
Even when intermittent cutting such as steel or cast iron is performed at high speed, especially with high calorific value, excellent cutting performance is maintained for a long time without uneven wear on the cutting edge, chipping and chipping (small chipping). The present invention relates to a surface-coated tungsten carbide-based cemented carbide cutting tool (hereinafter, referred to as a coated cemented carbide tool) that is exerted over a long period of time.
【０００２】[0002]
【従来の技術】従来、例えば特公昭５６−９３６５号公
報に記載されるように、内部が、重量％で（以下、％は
重量％を示す）、結合相形成成分として鉄族金属のうち
の１種以上：３〜３０重量％、第１分散相として周期律
表の４ａ、５ａ、および６ａ族金属の窒化物および炭窒
化物のうちの１種以上：２〜３０％、を含有し、残りが
第２分散相としての炭化タングステン（以下、ＷＣで示
す）と不可避不純物からなる組成を有し、かつ工具縦断
面で観察して、表面から２〜１００μｍの範囲内の所定
の幅に亘って、Ｃｏの最高含有量が上記内部のＣｏ含有
量に対する比率で１．１〜２．０の範囲内にあるが、上
記第１分散相が存在せず、結合相と上記第２分散相から
なる軟質表面帯域が存在するＷＣ基超硬合金基体（以
下、超硬基体と云う）の表面に、周期律表の４ａ、５
ａ、および６ａ族金属の炭化物、窒化物、および酸化
物、並びにこれらの２種以上の固溶体、さらに酸化アル
ミニウム（以下、Ａｌ2 Ｏ3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１〜２０
μｍの範囲内の所定の平均層厚で化学蒸着および／また
は物理蒸着してなる被覆超硬工具が、真空焼結法によっ
て製造され、かつ超硬基体に形成された上記表面２相組
織帯域によってすぐれた耐欠損性をもつことから、例え
ば鋼や鋳鉄などの断続切削に用いられていることも知ら
れている。2. Description of the Related Art Conventionally, as described in Japanese Patent Publication No. 56-9365, for example, the inside is expressed by weight% (hereinafter, "%" indicates weight%), and as a bonding phase forming component, among the iron group metals, One or more: 3 to 30% by weight, as a first dispersed phase, one or more of nitrides and carbonitrides of metals of groups 4a, 5a, and 6a of the periodic table: 2 to 30%, The remainder has a composition consisting of tungsten carbide (hereinafter referred to as WC) as a second dispersed phase and unavoidable impurities, and when observed in a longitudinal section of the tool, extends over a predetermined width within a range of 2 to 100 μm from the surface. The maximum content of Co is in the range of 1.1 to 2.0 in proportion to the internal Co content, but the first dispersed phase does not exist, and the combined phase and the second dispersed phase WC-based cemented carbide substrate having a soft surface zone (hereinafter referred to as a cemented carbide substrate) On the surface of, 4a of the periodic table, 5
a and carbides, nitrides and oxides of Group 6a metals, and two or more solid solutions thereof, and a single layer or two or more of aluminum oxide (hereinafter, referred to as Al 2 O 3 ) Hard coating layer consisting of multiple layers of
A coated cemented carbide tool obtained by chemical vapor deposition and / or physical vapor deposition with a predetermined average layer thickness in the range of μm is manufactured by the vacuum sintering method and is formed by the surface two-phase texture zone formed on the carbide substrate. Because of its excellent fracture resistance, it is also known that it is used for interrupted cutting of, for example, steel or cast iron.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の切削加工
の高能率化および省力化に対する要求は強く、これに伴
い、切削加工は高速化の傾向にあるが、上記従来被覆超
硬工具を断続切削に用いるのに際して、これを高速で行
うと、高速断続切削の場合大きな熱発生を伴うために、
切刃が熱塑性変形を起こし易く、この結果偏摩耗の進行
が著しく促進され、これが原因で比較的短時間で使用寿
命に至るのが現状である。On the other hand, in recent years, there has been a strong demand for higher efficiency and labor saving in cutting work, and with this, cutting work tends to be faster. When used for cutting, if this is performed at a high speed, large heat is generated in the case of high-speed interrupted cutting.
At present, the cutting edge is liable to undergo thermoplastic deformation, and as a result, the progress of uneven wear is remarkably promoted, and as a result, the service life of the cutting edge is relatively short in the present condition.
【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、耐熱塑性変形性のすぐれた被覆
超硬工具を開発すべく、特に上記のすぐれた耐欠損性を
有する従来被覆超硬工具に着目し、研究を行った結果、
超硬基体内部の組成を、結合相形成成分としてＣｏ：５
〜１２％、第１分散相として、ＴａとＺｒとＷとの炭化
物固溶体および炭窒化物固溶体［以下、それぞれ（Ｔ
ａ，Ｚｒ，Ｗ）Ｃ、（Ｔａ，Ｚｒ，Ｗ）ＣＮで示す］の
いずれか一方、あるいは両方、あるいはＴａとＺｒとＷ
とＭ（ただし、ＭはＴｉ、Ｎｂ、およびＣｒのうちの１
種または２種以上を示す）との炭化物固溶体および炭窒
化物固溶体［以下、それぞれ（Ｔａ，Ｚｒ，Ｗ，Ｍ）
Ｃ、（Ｔａ，Ｚｒ，Ｗ，Ｍ）ＣＮで示す］のいずれか一
方、または両方：５〜３０重量％、を含有し、残りが第
２分散相としてのＷＣと不可避不純物からなる組成に特
定した上で、これの真空焼結に際して、焼結温度への昇
温過程における少なくとも８００〜１３００℃の温度範
囲を圧力：１０〜５００ｔｏｒｒの窒素雰囲気とする
と、いずれも工具縦断面で観察して、表面から所定幅に
亘って、Ｃｏの最高含有量が上記内部のＣｏ含有量に比
して高いが、上記第１分散相の最低含有量が上記内部の
第１分散相の含有量に比して低い軟質表面帯域が形成さ
れると同時に、前記軟質表面帯域に隣接して、同じく所
定幅に亘って、Ｃｏの最低含有量は上記内部のＣｏ含有
量に比して低いが、上記第１分散相の最高含有量が上記
内部の第１分散相の含有量に比して高い硬質中間帯域が
形成されるようになり、この場合上記軟質表面帯域の
幅、並びにＣｏおよび第１分散相の含有比率、さらに上
記硬質中間帯域の幅、並びにＣｏおよび第１分散相の含
有比率は、いずれも上記超硬基体内部組成や焼結時の昇
温過程における窒素雰囲気導入温度範囲およびその窒素
圧力、さらに焼結温度などによって制御することがで
き、このように製造された超硬基体の表面に、化学蒸着
法および／または物理蒸着法を用いて、硬質被覆層、特
に望ましくはＴｉの炭化物（以下、ＴｉＣで示す）層、
窒化物（以下、ＴｉＮで示す）層、炭窒化物（以下、Ｔ
ｉＣＮで示す）層、炭酸化物（以下、ＴｉＣＯで示す）
層、窒酸化物（以下、ＴｉＮＯで示す）層、および炭窒
酸化物（以下、ＴｉＣＮＯで示す）層のうちの１種の単
層または２種以上の複層、さらに必要に応じてＡｌ2 Ｏ
3 層からなる硬質被覆層を形成すると、この結果の被覆
超硬工具は、超硬基体における上記軟質表面帯域によっ
てすぐれた耐欠損性が確保され、また上記硬質中間帯域
によって著しくすぐれた耐熱塑性変形性が確保され、し
たがって耐欠損性が要求される鋼や鋳鉄などの断続切削
を高速で行っても、高い熱発生にもかかわらず、切刃に
偏摩耗の発生なく、かつ欠けやチッピングなどの発生も
なく、すぐれた切削性能を長期に亘って発揮するように
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
From the above viewpoint, in order to develop a coated carbide tool with excellent heat-resistant plastic deformation properties, we focused on the conventional coated carbide tool with the above-mentioned excellent fracture resistance, and as a result of conducting research,
The composition inside the cemented carbide substrate was changed to Co: 5 as a binder phase forming component.
-12%, as a first dispersed phase, a carbide solid solution and a carbonitride solid solution of Ta, Zr and W [hereinafter, each of (T
a, Zr, W) C or (Ta, Zr, W) CN], or both, or Ta, Zr and W
And M (where M is one of Ti, Nb, and Cr)
Or two or more kinds) (hereinafter referred to as (Ta, Zr, W, M)
C, (Ta, Zr, W, M) CN] or both: 5 to 30% by weight, and the remainder is specified to be a composition comprising WC as the second dispersed phase and unavoidable impurities. Then, in vacuum sintering, when a temperature range of at least 800 to 1300 ° C. in a temperature rising process to a sintering temperature is set to a nitrogen atmosphere of pressure: 10 to 500 torr, all are observed in a tool longitudinal section, Over a predetermined width from the surface, the maximum content of Co is higher than the content of Co in the inside, but the minimum content of the first dispersed phase is smaller than the content of the first dispersed phase in the inside. At the same time as the soft surface zone is formed, the minimum content of Co is lower than the content of Co in the inside, but also over the predetermined width, adjacent to the soft surface zone. The highest content of the dispersed phase is that of the internal first dispersed phase. As a result, a high hard intermediate zone is formed as compared with the weight, and in this case, the width of the soft surface zone, and the content ratio of Co and the first dispersed phase, and the width of the hard intermediate zone, and Co and The content ratio of 1 dispersed phase can be controlled by the internal composition of the cemented carbide substrate, the nitrogen atmosphere introduction temperature range and the nitrogen pressure in the heating process during sintering, the nitrogen pressure, and the sintering temperature. Using a chemical vapor deposition method and / or a physical vapor deposition method, a hard coating layer, particularly preferably a Ti carbide (hereinafter, referred to as TiC) layer,
Nitride (hereinafter, referred to as TiN) layer, carbonitride (hereinafter, T
iCN) layer, carbonate (hereinafter referred to as TiCO)
Layer, a nitrided oxide (hereinafter referred to as TiNO) layer, and a carbonitride oxide (hereinafter referred to as TiCNO) single layer or two or more layers, and if necessary, Al 2 O
When a hard coating layer consisting of three layers is formed, the resulting coated cemented carbide tool has excellent fracture resistance secured by the soft surface zone of the cemented carbide substrate, and has a remarkably excellent thermal plastic deformation by the hard intermediate zone. Even when interrupted cutting of steel or cast iron that requires fracture resistance is performed at high speed, despite high heat generation, there is no uneven wear on the cutting edge and chipping and chipping etc. The research results showed that there would be no occurrence and that excellent cutting performance would be exhibited over a long period of time.
【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、内部が、結合相形成成分としてＣ
ｏ：５〜１２％、第１分散相として、（Ｔａ，Ｚｒ，
Ｗ）Ｃおよび／または（Ｔａ，Ｚｒ，Ｗ）ＣＮ、あるい
は（Ｔａ，Ｚｒ，Ｗ，Ｍ）Ｃおよび／または（Ｔａ，Ｚ
ｒ，Ｗ，Ｍ）ＣＮ［ただし、ＭはＴｉ、Ｎｂ、およびＣ
ｒのうちの１種または２種以上を示す］：５〜３０重量
％、を含有し、残りが第２分散相としてのＷＣと不可避
不純物からなる組成を有し、かつ工具縦断面で観察し
て、表面から１０〜５０μｍの範囲内の所定の幅に亘っ
て、Ｃｏの最高含有量が上記内部のＣｏ含有量に対する
比率で１．１〜１．５の範囲内にあり、かつ上記第１分
散相の最低含有量が上記内部の第１分散相の含有量に対
する比率で０．１〜０．８の範囲内にある軟質表面帯域
が存在し、さらに上記軟質表面帯域に隣接して、同じく
工具縦断面で観察して、１０〜２００μｍの範囲内の所
定の幅に亘って、Ｃｏの最低含有量が上記内部のＣｏ含
有量に対する比率で０．５〜１．０の範囲内にあり、か
つ上記第１分散相の最高含有量が上記内部の第１分散相
の含有量に対する比率で１．３〜３．０の範囲内にある
硬質中間帯域が存在する超硬基体の表面に、ＴｉＣ層、
ＴｉＮ層、ＴｉＣＮ層、ＴｉＣＯ層、ＴｉＮＯ層、およ
びＴｉＣＮＯ層のうちの１種の単層または２種以上の複
層、さらに必要に応じてＡｌ2 Ｏ3層からなる硬質被覆
層を５〜３０μｍの範囲内の所定の平均層厚で化学蒸着
および／または物理蒸着してなる、耐熱塑性変形性にす
ぐれ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-mentioned research results, and the inside thereof contains C as a binder phase forming component.
o: 5 to 12% as the first dispersed phase (Ta, Zr,
W) C and / or (Ta, Zr, W) CN, or (Ta, Zr, W, M) C and / or (Ta, Z)
r, W, M) CN [where M is Ti, Nb, and C
r represents one or more of r]]: 5 to 30% by weight, the remainder has a composition consisting of WC as the second dispersed phase and unavoidable impurities, and is observed in a tool longitudinal section. The maximum content of Co is within a range of 1.1 to 1.5 in a ratio to the internal Co content over a predetermined width within a range of 10 to 50 μm from the surface, and There is a soft surface zone in which the minimum content of the dispersed phase is in the range of 0.1 to 0.8 in a ratio to the content of the internal first dispersed phase, and further adjacent to the soft surface zone, Observed in a tool longitudinal section, over a predetermined width in the range of 10 to 200 μm, the minimum content of Co is in the range of 0.5 to 1.0 in proportion to the internal Co content, And the ratio of the highest content of the first dispersed phase to the content of the internal first dispersed phase A TiC layer on the surface of the cemented carbide substrate having a hard intermediate zone in the range of 1.3 to 3.0.
A hard coating layer composed of a single layer or two or more layers of a TiN layer, a TiCN layer, a TiCO layer, a TiNO layer, and a TiCNO layer, and if necessary, an Al 2 O 3 layer of 5 to 30 μm. Is characterized by a coated carbide tool having excellent heat-resistant plastic deformation properties, which is obtained by chemical vapor deposition and / or physical vapor deposition with a predetermined average layer thickness in the range of
【０００６】つぎに、この発明の被覆超硬工具におい
て、超硬基体の内部組成、並びに超硬基体における軟質
表面帯域および硬質中間帯域の幅、Ｃｏの含有比率、お
よび第１分散相の含有比率、さらに硬質被覆層の平均層
厚を上記の通りに限定した理由を説明する。 （Ａ）超硬基体の内部組成 Ｃｏ成分は焼結性を促進させて、強度を向上させるのに
不可欠の成分であるが、その含有量が５％未満では、所
望の強度を確保することができず、一方その含有量が１
２％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５〜１２％、望ましくは６〜１
０％と定めた。また、第１分散相には、硬さを向上さ
せ、もって耐摩耗性を向上させる作用があるが、その含
有量が５％未満では、所望の耐摩耗性向上効果が得られ
ず、一方その含有量が３０％を越えると、切刃の耐欠損
性が低下するようになることから、その含有量を５〜３
０％、望ましくは１０〜２０％と定めた。[0006] Next, in the coated cemented carbide tool of the present invention, the internal composition of the cemented carbide substrate, the width of the soft surface zone and the hard intermediate zone, the content ratio of Co, and the content ratio of the first dispersed phase in the cemented carbide substrate. The reason why the average thickness of the hard coating layer is further limited as described above will be described. (A) Internal Composition of Carbide Substrate The Co component is an indispensable component for promoting sinterability and improving strength, but if its content is less than 5%, desired strength may be secured. No, but the content is 1
If the content exceeds 2%, the wear resistance rapidly decreases, so the content is 5 to 12%, preferably 6 to 1%.
It was set to 0%. Further, the first dispersed phase has an effect of improving the hardness and thus the wear resistance. However, if the content is less than 5%, the desired effect of improving the wear resistance cannot be obtained. If the content exceeds 30%, the chipping resistance of the cutting edge is reduced, so that the content is 5 to 3%.
0%, preferably 10 to 20%.
【０００７】（Ｂ）軟質表面帯域 その幅が１０μｍ未満になったり、またＣｏの最高含有
比率が１．１未満になったり、さらに第１分散相の最低
含有比率が０．８を越えたりすると、耐欠損性に所望の
向上効果が得られず、一方その幅が５０μｍを越えた
り、またＣｏの最高含有比率が１．５を越えたり、さら
に第１分散相の最低含有比率が０．１未満になったりす
ると、この帯域で熱塑性変形が発生するようになること
から、その幅を１０〜５０μｍ、望ましくは２０〜３５
μｍ，Ｃｏの最高含有比率を１．１〜１．５、望ましく
は１．２〜１．４、そして第１分散相の最低含有比率を
０．１〜０．８、望ましくは０．２〜０．６とそれぞれ
定めた。(B) Soft surface zone If the width is less than 10 μm, if the maximum content of Co is less than 1.1, or if the minimum content of the first dispersed phase exceeds 0.8, The desired effect of improving the fracture resistance cannot be obtained, while the width exceeds 50 μm, the maximum Co content exceeds 1.5, and the minimum content ratio of the first dispersed phase is 0.1%. If the width is less than 1, thermoplastic deformation occurs in this zone, so that the width is 10 to 50 μm, preferably 20 to 35 μm.
The maximum content of μm and Co is 1.1 to 1.5, preferably 1.2 to 1.4, and the minimum content of the first dispersed phase is 0.1 to 0.8, preferably 0.2 to 0.8. 0.6 respectively.
【０００８】（Ｃ）硬質中間帯域 その幅が１０μｍ未満でも、またＣｏの最低含有比率が
１．０を越えても、さらに第１分散相の最高含有比率が
１．３未満でも所望のすぐれた耐熱塑性変形性を確保す
ることができず、一方その幅が２００μｍを越えたり、
またＣｏの最低含有比率が０．５未満になったり、さら
に第１分散相の最高含有比率が３．０を越えたりする
と、切刃の耐欠損性が低下するようになることから、そ
の幅を１０〜２００μｍ、望ましくは５０〜１５０μ
ｍ，Ｃｏの最低含有比率を０．５〜１．０、望ましくは
０．６〜０．８、そして第１分散相の最高含有比率を
１．３〜３．０、望ましくは１．６〜２．６とそれぞれ
定めた。(C) Hard intermediate zone Even if the width is less than 10 μm, the minimum content of Co exceeds 1.0, and the maximum content of the first dispersed phase is less than 1.3, the desired excellent condition is obtained. Heat-resistant plastic deformation cannot be ensured, while its width exceeds 200 μm,
Further, when the minimum content ratio of Co is less than 0.5 or the maximum content ratio of the first dispersed phase exceeds 3.0, the chipping resistance of the cutting edge decreases, so that the width of the cutting edge decreases. 10 to 200 μm, desirably 50 to 150 μm
The minimum content ratio of m and Co is 0.5 to 1.0, desirably 0.6 to 0.8, and the maximum content ratio of the first dispersed phase is 1.3 to 3.0, desirably 1.6 to 1.0. 2.6 respectively.
【０００９】（Ｄ）硬質被覆層の平均層厚 その厚さが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、一方その厚さが３０μｍを越え
ると、耐欠損性が低下するようになることから、その厚
さを５〜３０μｍ、望ましくは７〜２０μｍと定めた。(D) Average Layer Thickness of Hard Coating Layer If the thickness is less than 5 μm, the desired excellent abrasion resistance cannot be ensured, while if the thickness exceeds 30 μm, the fracture resistance becomes poor. The thickness is determined to be 5 to 30 μm, and preferably 7 to 20 μm, since the thickness decreases.
【００１０】[0010]
【発明の実施の形態】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、平均粒径：
３μｍの中粒ＷＣ粉末、同６μｍの粗粒ＷＣ粉末、同
１．２μｍの（Ｔｉ，Ｗ）ＣＮ［重量比（以下同じ）
で、ＴｉＣ／ＴｉＮ／ＷＣ＝２４／２０／５６］粉末、
同１．５μｍの（Ｔａ，Ｎｂ）Ｃ［ＴａＣ／ＮｂＣ＝９
０／１０］粉末、同１．３μｍのＴａＣ粉末、同１．５
μｍのＺｒＣ粉末、同２．０μｍのＣｒ3 Ｃ2 粉末、お
よび同１．２μｍの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、この混合粉末を所定形状
の圧粉体にプレス成形し、ついでこの圧粉体を同じく表
１に示される条件で焼結し、焼結体に仕上げ加工および
ホーニング加工を施すことにより、いずれもＩＳＯ規格
ＣＮＭＧ１２０４０８に則したスローアウエイチップ形
状をもった超硬基体Ａ〜Ｌをそれぞれ製造した。また、
比較の目的で、表２に示される通り、焼結温度への昇温
過程での窒素雰囲気の導入を行わず、いずれも真空雰囲
気での焼結を行う以外は同一の条件で超硬基体ａ〜ｌを
それぞれ製造した。BEST MODE FOR CARRYING OUT THE INVENTION A coated carbide tool according to the present invention will be specifically described with reference to examples. As raw material powder, average particle size:
3 μm medium WC powder, 6 μm coarse WC powder, 1.2 μm (Ti, W) CN [weight ratio (the same applies hereinafter)]
And TiC / TiN / WC = 24/20/56] powder,
1.5 μm (Ta, Nb) C [TaC / NbC = 9
0/10] powder, 1.3 μm TaC powder, 1.5 μm
A ZrC powder of 2.0 μm, a Cr 3 C 2 powder of 2.0 μm, and a Co powder of 1.2 μm were prepared, and these raw material powders were blended in the composition shown in Table 1, followed by ball milling.
After being wet-mixed for hours and dried, the mixed powder is pressed into a green compact having a predetermined shape, and then the green compact is sintered under the conditions shown in Table 1, and the sintered body is finished and honed. By performing the processing, the super hard bases A to L each having a throw-away tip shape conforming to the ISO standard CNMG120408 were manufactured. Also,
For the purpose of comparison, as shown in Table 2, the cemented carbide substrate a was obtained under the same conditions except that the nitrogen atmosphere was not introduced in the process of raising the temperature to the sintering temperature and sintering was performed in a vacuum atmosphere. ~ L were each manufactured.
【００１１】ついで、これらの超硬基体Ａ〜Ｌおよび超
硬基体ａ〜ｌの表面に、通常の外熱式化学蒸着装置およ
び物理蒸着装置の１種であるイオンプレーティング装置
を用い、表３、４に示される通りの組成および平均層厚
の硬質被覆層を形成することにより本発明被覆超硬工具
１〜１２および比較被覆超硬工具１〜１２をそれぞれ製
造した。Next, on the surfaces of these super-hard substrates A to L and super-hard substrates a to l, an ion plating apparatus, which is one of ordinary external thermal chemical vapor deposition apparatuses and physical vapor deposition apparatuses, is used. By forming a hard coating layer having the composition and the average layer thickness as shown in Nos. 4 and 4, coated carbide tools 1 to 12 of the present invention and comparative coated carbide tools 1 to 12 were produced, respectively.
【００１２】この結果得られた本発明被覆超硬工具１〜
１２および比較被覆超硬工具１〜１２について、 （ａ）超硬基体内部の組成は、まず工具縦断面における
中心部任意箇所の組織写真を走査型電子顕微鏡を用いて
撮り、この組織写真における実質的にＣｏからなる結合
相、第１分散相、および第２分散相であるＷＣの割合
（面積％）を画像解析装置を用いて算出し、この算出結
果と、オージェ電子分光分析装置を用いて測定した第１
分散相構成成分の分析値（原子％）から、重量割合（重
量％）に換算することにより求めた。 （ｂ）また、同じく工具縦断面における軟質表面帯域お
よび硬質中間帯域の幅は光学顕微鏡組織写真を用いて測
定し、さらにこれらの帯域におけるＣｏの最高および最
低含有比率および第１分散相の最高および最低含有比率
は、エネルギー分散型Ｘ線測定装置を用いて、表面から
内部へ向かってのＣｏおよび第１分散相構成成分の含有
量の連続変化曲線を求め、この結果と上記の超硬基体内
部のＣｏおよび第１分散相の含有量から求めた。 以上（ａ）および（ｂ）にもとづいて超硬基体内部の組
成、さらに工具縦断面における軟質表面帯域および硬質
中間帯域の幅、Ｃｏの含有比率、および第１分散相の含
有比率を求めた。これらの結果を表５、６に示した。ま
た表５、６には超硬基体内部の硬さ（ロックウエル硬さ
Ａスケール）も合わせて示した。The resulting coated carbide tools 1 to 5 of the present invention
12 and Comparative Coated Carbide Tools 1 to 12: (a) The composition of the inside of the carbide substrate was determined by first taking a photograph of the structure at an arbitrary position at the center in the longitudinal section of the tool using a scanning electron microscope. The ratio (area%) of WC as the binder phase, the first dispersed phase, and the second dispersed phase composed of Co is calculated using an image analyzer, and the calculation result is used together with an Auger electron spectroscopic analyzer. First measured
It was determined by converting the analysis value (atomic%) of the constituent components of the dispersed phase into a weight ratio (% by weight). (B) Similarly, the widths of the soft surface zone and the hard intermediate zone in the tool longitudinal section were measured using optical micrographs, and the maximum and minimum content ratios of Co and the maximum and minimum contents of the first dispersed phase in these zones were also measured. The minimum content ratio was determined by calculating a continuous change curve of the contents of Co and the first dispersed phase component from the surface to the inside using an energy dispersive X-ray measuring apparatus. Of the first dispersed phase. Based on the above (a) and (b), the composition inside the cemented carbide substrate, the width of the soft surface zone and the hard intermediate zone in the tool longitudinal section, the content ratio of Co, and the content ratio of the first dispersed phase were determined. Tables 5 and 6 show these results. Tables 5 and 6 also show the hardness inside the carbide substrate (Rockwell hardness A scale).
【００１３】さらに、上記本発明被覆超硬工具１〜１２
および比較被覆超硬工具１〜１２について、 被削材：ＳＣＭ４４０（ブリネル硬さ：２２０）の長手
方向等間隔４本縦溝入り丸棒、 切削速度：４２０ｍ／ｍｉｎ、 送り：０．２８ｍｍ、 切り込み：１．５ｍｍ、 の条件で鋼の乾式高速断続切削試験を行い、使用寿命に
至るまでの切削時間を測定した。これらの測定結果を表
５、６に示した。Further, the above-mentioned coated carbide tools 1 to 12 according to the present invention.
Workpiece: SCM440 (Brinell hardness: 220), round bar with four longitudinal grooves at regular intervals in the longitudinal direction, cutting speed: 420 m / min, feed: 0.28 mm, cutting : 1.5 mm, a dry high-speed intermittent cutting test of steel was performed, and the cutting time until the service life was measured. Tables 5 and 6 show the results of these measurements.
【００１４】[0014]
【表１】 [Table 1]
【００１５】[0015]
【表２】 [Table 2]
【００１６】[0016]
【表３】 [Table 3]
【００１７】[0017]
【表４】 [Table 4]
【００１８】[0018]
【表５】 [Table 5]
【００１９】[0019]
【表６】 [Table 6]
【００２０】[0020]
【発明の効果】表５、６に示される結果から、本発明被
覆超硬工具１〜１２は、いずれも超硬基体における硬質
中間帯域の存在によって熱発生の高い鋼の高速断続切削
でも切刃の熱塑性変形が著しく抑制され、軟質表面帯域
によるすぐれた耐欠損性と相まって、切刃は正常摩耗を
示すため、長期に亘ってすぐれた切削性能を発揮するの
に対して、比較被覆超硬工具１〜１２は、いずれも軟質
表面帯域は存在するが、前記硬質中間帯域が存在しない
ために、大きな発熱量を伴う高速断続切削では切刃に熱
塑性変形が発生し、これが原因で切刃の偏摩耗が促進
し、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、すぐれた耐熱塑
性変形性と耐欠損性を合わせもつので、鋼や鋳鉄などの
通常の条件での連続切削や断続切削は勿論のこと、これ
らの切削を高速で行っても切刃に欠けやチッピングなど
の発生なく、正常摩耗を示し、したがって切削加工の高
能率化および省力化に十分満足に対応することができる
ものである。According to the results shown in Tables 5 and 6, the coated carbide tools 1 to 12 according to the present invention can be used for cutting edge even in high-speed interrupted cutting of steel with high heat generation due to the presence of the hard intermediate zone in the carbide substrate. The cutting edge shows normal wear, in combination with the excellent fracture resistance due to the soft surface zone, and exhibits excellent cutting performance over a long period of time, while the comparative coated carbide tool In Nos. 1 to 12, although a soft surface zone exists, but the hard intermediate zone does not exist, thermoplastic deformation occurs in the cutting edge in high-speed interrupted cutting with a large amount of heat generation. It is clear that abrasion is accelerated, leading to a short service life in a short time. As described above, the coated carbide tool of the present invention has excellent heat-resistant plastic deformation resistance and fracture resistance, so that not only continuous cutting and interrupted cutting under ordinary conditions such as steel and cast iron, but also Even when the cutting is performed at high speed, the cutting edge shows normal wear without chipping, chipping, etc., and therefore can sufficiently cope with high efficiency and labor saving of cutting.
───────────────────────────────────────────────────── 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 (72)発明者 ▲功▼刀 斉 茨城県結城郡石下町大字古間木1511番地 三菱マテリアル株式会社筑波製作所内 (72)発明者 濱口 雄樹 茨城県結城郡石下町大字古間木1511番地 三菱マテリアル株式会社筑波製作所内──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 6 Identification code FI C23C 16/30 C23C 16/30 (72) Inventor ▲ Isao Toshi 1511 Furimagi, Ishishita-cho, Yuki-gun, Ibaraki Prefecture Mitsubishi Materials Corporation (72) Inventor, Yuki Hamaguchi, 1511 Furamaki, Ishishita-cho, Yuki-gun, Ibaraki Pref., Mitsubishi Materials Corporation Tsukuba Works
Claims (4)
び炭窒化物固溶体のいずれか一方、または両方：５〜３
０重量％、を含有し、残りが第２分散相としての炭化タ
ングステンと不可避不純物からなる組成を有し、 かつ工具縦断面で観察して、表面から１０〜５０μｍの
範囲内の所定の幅に亘って、Ｃｏの最高含有量が上記内
部のＣｏ含有量に対する比率で１．１〜１．５の範囲内
にあり、かつ上記第１分散相の最低含有量が上記内部の
第１分散相の含有量に対する比率で０．１〜０．８の範
囲内にある軟質表面帯域が存在し、 さらに上記軟質表面帯域に隣接して、同じく工具縦断面
で観察して、１０〜２００μｍの範囲内の所定の幅に亘
って、Ｃｏの最低含有量が上記内部のＣｏ含有量に対す
る比率で０．５〜１．０の範囲内にあり、かつ上記第１
分散相の最高含有量が上記内部の第１分散相の含有量に
対する比率で１．３〜３．０の範囲内にある硬質中間帯
域が存在する炭化タングステン基超硬合金基体の表面
に、 Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、
窒酸化物層、および炭窒酸化物層のうちの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５〜３０μｍ
の範囲内の所定の平均層厚で化学蒸着および／または物
理蒸着してなる、耐熱塑性変形性にすぐれた表面被覆炭
化タングステン基超硬合金製切削工具。1. The interior is composed of 5 to 12% by weight of Co as a binder phase forming component, and one or both of a carbide solid solution and a carbonitride solid solution of Ta, Zr and W as a first dispersed phase. 3
0% by weight, with the balance having the composition of tungsten carbide as the second dispersed phase and unavoidable impurities, and having a predetermined width within a range of 10 to 50 μm from the surface when observed in a longitudinal section of the tool. The highest content of Co is in the range of 1.1 to 1.5 in the ratio to the content of Co in the inside, and the lowest content of the first dispersed phase is the content of the first dispersed phase in the inside. There is a soft surface zone in the range of 0.1 to 0.8 in the ratio to the content, and further, adjacent to the soft surface zone, similarly observed in the tool longitudinal section, in the range of 10 to 200 μm. Over a predetermined width, the minimum content of Co is in the range of 0.5 to 1.0 as a ratio to the internal Co content, and
The surface of the tungsten carbide-based cemented carbide substrate having a hard intermediate zone in which the maximum content of the dispersed phase is in the range of 1.3 to 3.0 in the ratio to the content of the internal first dispersed phase, Carbide layers, nitride layers, carbonitride layers, carbonate layers,
A hard coating layer composed of a single layer or a multilayer of two or more of a nitric oxide layer and a carbonitride layer;
A cutting tool made of a surface-coated tungsten carbide-based cemented carbide having excellent heat-resistant plastic deformation properties, which is formed by chemical vapor deposition and / or physical vapor deposition with a predetermined average layer thickness in the range described above.
び炭窒化物固溶体のいずれか一方、または両方：５〜３
０重量％、を含有し、残りが第２分散相としての炭化タ
ングステンと不可避不純物からなる組成を有し、 かつ工具縦断面で観察して、表面から１０〜５０μｍの
範囲内の所定の幅に亘って、Ｃｏの最高含有量が上記内
部のＣｏ含有量に対する比率で１．１〜１．５の範囲内
にあり、かつ上記第１分散相の最低含有量が上記内部の
第１分散相の含有量に対する比率で０．１〜０．８の範
囲内にある軟質表面帯域が存在し、 さらに上記軟質表面帯域に隣接して、同じく工具縦断面
で観察して、１０〜２００μｍの範囲内の所定の幅に亘
って、Ｃｏの最低含有量が上記内部のＣｏ含有量に対す
る比率で０．５〜１．０の範囲内にあり、かつ上記第１
分散相の最高含有量が上記内部の第１分散相の含有量に
対する比率で１．３〜３．０の範囲内にある硬質中間帯
域が存在する炭化タングステン基超硬合金基体の表面
に、 Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、
窒酸化物層、および炭窒酸化物層のうちの１種の単層ま
たは２種以上の複層と、酸化アルミニウム層からなる硬
質被覆層を５〜３０μｍの範囲内の所定の平均層厚で化
学蒸着および／または物理蒸着してなる、耐熱塑性変形
性にすぐれた表面被覆炭化タングステン基超硬合金製切
削工具。2. The interior contains 5 to 12% by weight of Co as a binder phase forming component, and one or both of a carbide solid solution and a carbonitride solid solution of Ta, Zr and W as a first dispersed phase. 3
0% by weight, with the balance having the composition of tungsten carbide as the second dispersed phase and unavoidable impurities, and having a predetermined width within a range of 10 to 50 μm from the surface when observed in a longitudinal section of the tool. The highest content of Co is in the range of 1.1 to 1.5 in the ratio to the content of Co in the inside, and the lowest content of the first dispersed phase is the content of the first dispersed phase in the inside. There is a soft surface zone in the range of 0.1 to 0.8 in the ratio to the content, and further, adjacent to the soft surface zone, similarly observed in the tool longitudinal section, in the range of 10 to 200 μm. Over a predetermined width, the minimum content of Co is in the range of 0.5 to 1.0 as a ratio to the internal Co content, and
The surface of the tungsten carbide-based cemented carbide substrate having a hard intermediate zone in which the maximum content of the dispersed phase is in the range of 1.3 to 3.0 in the ratio to the content of the internal first dispersed phase, Carbide layers, nitride layers, carbonitride layers, carbonate layers,
A hard coating layer composed of a single layer or two or more layers of a nitrogen oxide layer and a carbonitride layer, and an aluminum oxide layer with a predetermined average layer thickness in the range of 5 to 30 μm; A cutting tool made of surface-coated tungsten carbide-based cemented carbide with excellent heat-resistant plastic deformation properties, formed by chemical vapor deposition and / or physical vapor deposition.
ｉ、Ｎｂ、およびＣｒのうちの１種または２種以上を示
す）との炭化物固溶体および炭窒化物固溶体のいずれか
一方、または両方：５〜３０重量％、を含有し、残りが
第２分散相としての炭化タングステンと不可避不純物か
らなる組成を有し、 かつ工具縦断面で観察して、表面から１０〜５０μｍの
範囲内の所定の幅に亘って、Ｃｏの最高含有量が上記内
部のＣｏ含有量に対する比率で１．１〜１．５の範囲内
にあり、かつ上記第１分散相の最低含有量が上記内部の
第１分散相の含有量に対する比率で０．１〜０．８の範
囲内にある軟質表面帯域が存在し、 さらに上記軟質表面帯域に隣接して、同じく工具縦断面
で観察して、１０〜２００μｍの範囲内の所定の幅に亘
って、Ｃｏの最低含有量が上記内部のＣｏ含有量に対す
る比率で０．５〜１．０の範囲内にあり、かつ上記第１
分散相の最高含有量が上記内部の第１分散相の含有量に
対する比率で１．３〜３．０の範囲内にある硬質中間帯
域が存在する炭化タングステン基超硬合金基体の表面
に、 Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、
窒酸化物層、および炭窒酸化物層のうちの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５〜３０μｍ
の範囲内の所定の平均層厚で化学蒸着および／または物
理蒸着してなる、耐熱塑性変形性にすぐれた表面被覆炭
化タングステン基超硬合金製切削工具。3. The interior contains 5 to 12% by weight of Co as a binder phase-forming component, and Ta, Zr, W and M as a first dispersed phase (where M is T
i, Nb, and / or Cr), and either or both of a carbide solid solution and a carbonitride solid solution: 5 to 30% by weight; It has a composition consisting of tungsten carbide as a phase and unavoidable impurities, and when observed in a longitudinal section of the tool, over a predetermined width within a range of 10 to 50 μm from the surface, the maximum content of Co is such that The minimum content of the first dispersed phase is in the range of 1.1 to 1.5 in a ratio to the content, and the minimum content of the first dispersed phase is 0.1 to 0.8 in a ratio to the content of the internal first dispersed phase. There is a soft surface zone in the range, and further, adjacent to the soft surface zone, also observed in the tool longitudinal section, over a predetermined width in the range of 10 to 200 μm, the minimum content of Co is 0.5 to 0.5% of the internal Co content In the range of 2.0, and the first
The surface of the tungsten carbide-based cemented carbide substrate having a hard intermediate zone in which the maximum content of the dispersed phase is in the range of 1.3 to 3.0 in the ratio to the content of the internal first dispersed phase, Carbide layers, nitride layers, carbonitride layers, carbonate layers,
A hard coating layer composed of a single layer or a multilayer of two or more of a nitric oxide layer and a carbonitride layer;
A cutting tool made of a surface-coated tungsten carbide-based cemented carbide having excellent heat-resistant plastic deformation properties, which is formed by chemical vapor deposition and / or physical vapor deposition with a predetermined average layer thickness in the range described above.
〜１２重量％、 第１分散相としてＴａとＺｒとＷとＭ（ただし、ＭはＴ
ｉ、Ｎｂ、およびＣｒのうちの１種または２種以上を示
す）との炭化物固溶体および炭窒化物固溶体ののいずれ
か一方、または両方：５〜３０重量％、を含有し、残り
が第２分散相としての炭化タングステンと不可避不純物
からなる組成を有し、 かつ工具縦断面で観察して、表面から１０〜５０μｍの
範囲内の所定の幅に亘って、Ｃｏの最高含有量が上記内
部のＣｏ含有量に対する比率で１．１〜１．５の範囲内
にあり、かつ上記第１分散相の最低含有量が上記内部の
第１分散相の含有量に対する比率で０．１〜０．８の範
囲内にある軟質表面帯域が存在し、 さらに上記軟質表面帯域に隣接して、同じく工具縦断面
で観察して、１０〜２００μｍの範囲内の所定の幅に亘
って、Ｃｏの最低含有量が上記内部のＣｏ含有量に対す
る比率で０．５〜１．０の範囲内にあり、かつ上記第１
分散相の最高含有量が上記内部の第１分散相の含有量に
対する比率で１．３〜３．０の範囲内にある硬質中間帯
域が存在する炭化タングステン基超硬合金基体の表面
に、 Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、
窒酸化物層、および炭窒酸化物層のうちの１種の単層ま
たは２種以上の複層と、酸化アルミニウム層からなる硬
質被覆層を５〜３０μｍの範囲内の所定の平均層厚で化
学蒸着および／または物理蒸着してなる、耐熱塑性変形
性にすぐれた表面被覆炭化タングステン基超硬合金製切
削工具。4. Co: 5 as a bonding phase forming component.
~ 12 wt%, Ta, Zr, W and M as the first dispersed phase (where M is T
one or more of i, Nb, and Cr), and either or both of a carbide solid solution and a carbonitride solid solution: 5 to 30% by weight; It has a composition consisting of tungsten carbide as a disperse phase and unavoidable impurities, and when observed in a longitudinal section of the tool, over a predetermined width in the range of 10 to 50 μm from the surface, the highest content of Co in the inside is The minimum content of the first dispersed phase is within a range of 1.1 to 1.5 in terms of the Co content, and the minimum content of the first dispersed phase is 0.1 to 0.8 in terms of the content of the internal first dispersed phase. The soft surface zone exists in the range of, and the minimum content of Co over a predetermined width in the range of 10 to 200 μm, which is also observed in the tool longitudinal section adjacent to the soft surface zone. Is a ratio of 0.5 to the internal Co content. In the range of 1.0, and the first
The surface of the tungsten carbide-based cemented carbide substrate having a hard intermediate zone in which the maximum content of the dispersed phase is in the range of 1.3 to 3.0 in the ratio to the content of the internal first dispersed phase, Carbide layers, nitride layers, carbonitride layers, carbonate layers,
A hard coating layer composed of a single layer or two or more layers of a nitrogen oxide layer and a carbonitride layer, and an aluminum oxide layer with a predetermined average layer thickness in the range of 5 to 30 μm; A cutting tool made of surface-coated tungsten carbide-based cemented carbide with excellent heat-resistant plastic deformation properties, formed by chemical vapor deposition and / or physical vapor deposition.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20310997A JP3331916B2 (en) | 1997-07-29 | 1997-07-29 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent heat plastic deformation |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP20310997A JP3331916B2 (en) | 1997-07-29 | 1997-07-29 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent heat plastic deformation |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH1142504A true JPH1142504A (en) | 1999-02-16 |
| JP3331916B2 JP3331916B2 (en) | 2002-10-07 |
Family
ID=16468554
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP20310997A Ceased JP3331916B2 (en) | 1997-07-29 | 1997-07-29 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent heat plastic deformation |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3331916B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011177801A (en) * | 2010-02-26 | 2011-09-15 | Mitsubishi Materials Corp | Surface-coated wc-based cemented carbide insert |
| JP2011235370A (en) * | 2010-05-07 | 2011-11-24 | Mitsubishi Materials Corp | Surface-coated wc-based cemented carbide insert |
-
1997
- 1997-07-29 JP JP20310997A patent/JP3331916B2/en not_active Ceased
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011177801A (en) * | 2010-02-26 | 2011-09-15 | Mitsubishi Materials Corp | Surface-coated wc-based cemented carbide insert |
| JP2011235370A (en) * | 2010-05-07 | 2011-11-24 | Mitsubishi Materials Corp | Surface-coated wc-based cemented carbide insert |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3331916B2 (en) | 2002-10-07 |
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