JP3331916B2 - Surface coated tungsten carbide based cemented carbide cutting tool with excellent heat plastic deformation - Google Patents
Surface coated tungsten carbide based cemented carbide cutting tool with excellent heat plastic deformationInfo
- Publication number
- JP3331916B2 JP3331916B2 JP20310997A JP20310997A JP3331916B2 JP 3331916 B2 JP3331916 B2 JP 3331916B2 JP 20310997 A JP20310997 A JP 20310997A JP 20310997 A JP20310997 A JP 20310997A JP 3331916 B2 JP3331916 B2 JP 3331916B2
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- Japan
- Prior art keywords
- content
- dispersed phase
- range
- layers
- carbide
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- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
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、Ａｌ2Ｏ3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１〜２０μ
ｍ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 formed by chemical vapor deposition and / or physical vapor deposition with a predetermined average layer thickness in the range of m 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、（Ｔ
ａ，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、ＴｉＣＮ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Ａｌ2Ｏ3 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, W and M (where M represents one or more of Ti, Nb and Cr) [ Hereinafter, (Ta, Zr, W, M) C, (T
a, 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. At the time of 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 longitudinal section of the tool, and a predetermined value Over the width,
A soft surface zone is formed in which the highest content of Co is higher than the content of Co in the inside, but the lowest content of the first dispersed phase is lower than the content of the first dispersed phase in the inside. At the same time, adjacent to the soft surface zone and over the same predetermined width, the minimum content of Co is lower than the internal Co content, but the maximum content of the first dispersed phase is higher than the above. A hard intermediate zone is formed that is higher than the content of the internal first dispersed phase, in which case the width of the soft surface zone, the content ratio of Co and the first dispersed phase, and the hard intermediate zone are further increased. And the content ratio of Co and the first dispersed phase are
Each of them 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, a nitride (hereinafter referred to as TiN) layer, a carbonitride (hereinafter referred to as , TiCN), a carbonate (hereinafter referred to as TiCO) layer, a nitride (hereinafter referred to as TiNO) layer, and a carbonitride (hereinafter referred to as TiCNO) layer Layer or two
By forming a hard coating layer composed of at least two or more layers and, if necessary, an Al 2 O 3 layer, the resulting coated cemented carbide tool has excellent fracture resistance due to the soft surface zone in the cemented carbide substrate. In addition, the above-mentioned hard intermediate zone ensures remarkably excellent thermal plastic deformation resistance, and therefore, even when performing high-speed intermittent cutting of steel or cast iron, which requires fracture resistance, despite high heat generation, cutting Research results have shown that the blades can exhibit excellent cutting performance over a long period of time without causing uneven wear on the blades and without chipping or chipping.
【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，Ｍ）Ｃおよび／または（Ｔａ，Ｚｒ，Ｗ，Ｍ）ＣＮ
［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］：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、Ｃ
ｏ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Ａｌ2Ｏ3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, M) C and / or (Ta, Zr, W, M) CN
[However, M represents one or more of Ti, Nb, and Cr]: 5 to 30% by weight, and the remainder is composed of WC as the second dispersed phase and unavoidable impurities. Have, and observe in the tool longitudinal section, from the surface 10 to
Over a predetermined width in the range of 50 μm, the maximum content of Co is 1.1 to 1.
5, and the minimum content of the first dispersed phase is 0.1 to 0.1 to the content of the internal first dispersed phase.
There is a soft surface zone in the range of 0.8, and also adjacent to the soft surface zone, also observed in the tool longitudinal section, over a predetermined width in the range of 10-200 μm, C
The minimum content of o is in the range of 0.5 to 1.0 in proportion to the content of the internal Co, and the maximum content of the first dispersed phase is based on the content of the internal first dispersed phase. A TiC layer, a TiN layer, and a TiCN layer are formed on the surface of a cemented carbide substrate having a hard intermediate zone having a ratio in a range of 1.3 to 3.0.
Layer, a TiCO layer, a TiNO layer, and a TiCNO layer, a single layer or two or more layers, and if necessary, a hard coating layer composed of an Al 2 O 3 layer in a range of 5 to 30 μm. The present invention is characterized by a coated carbide tool 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.
【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Ｃｒ3Ｃ2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Ｃ
ＮＭＧ１２０４０８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〜Ｆ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〜ｆ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 and wet-mixed in a ball mill for 72 hours. After drying, the mixed powder was press-molded into a green compact of a predetermined shape.
By sintering under the conditions shown in Table 1 and finishing and honing the sintered body,
Carbide substrates A to F having a throw-away tip shape according to NMG120408 were manufactured. Also, for comparison purposes, as shown in Table 2, the nitrogen atmosphere was not introduced in the process of raising the temperature to the sintering temperature, and the carbide was sintered under the same conditions except that the sintering was performed in a vacuum atmosphere. Substrates a to f were respectively manufactured.
【００１１】ついで、これらの超硬基体Ａ〜Ｆおよび超
硬基体ａ〜ｆ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
１〜６および比較被覆超硬工具１〜６をそれぞれ製造し
た。Then, the surfaces of the super-hard substrates A to F and the super-hard substrates a to f were subjected to ion plating using one of ordinary external thermal chemical vapor deposition devices and physical vapor deposition devices. By forming a hard coating layer having the composition and average layer thickness as shown in Nos. 4 and 4, coated carbide tools 1 to 6 of the present invention and comparative coated carbide tools 1 to 6 were produced, respectively.
【００１２】この結果得られた本発明被覆超硬工具１〜
６および比較被覆超硬工具１〜６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
6 and comparative coated carbide tools 1 to 6: (a) The composition of the inside of the carbide substrate was determined by first taking a photograph of the structure at an arbitrary position in the center of 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,
Furthermore, the width of the soft surface zone and the hard intermediate zone in the longitudinal section of the tool, 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１〜６お
よび比較被覆超硬工具１〜６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, regarding the above-mentioned coated carbide tools 1 to 6 of the present invention and comparative coated carbide tools 1 to 6, a work material: SCM440 (Brinell hardness: 220), a round bar having four longitudinal grooves at equal intervals in the longitudinal direction. Under a condition of: cutting speed: 420 m / min, feed: 0.28 mm, cutting depth: 1.5 mm, a dry high-speed interrupted cutting test of steel was performed, and a cutting time until a 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１〜６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１〜６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 6 according to the present invention can be used 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. In all of Nos. 1 to 6, the soft surface zone exists, but the hard intermediate zone does not exist, so that high-speed intermittent cutting with a large amount of heat generates thermoplastic deformation of the cutting edge. It is clear that abrasion is accelerated, leading to a short service life in a short time. As described above, the coated cemented carbide tool of the present invention has excellent heat-resistant plastic deformation properties 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.7 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 審査官 間中 耕治 (56)参考文献 特開 平７−180071（ＪＰ，Ａ) 特開 昭63−114970（ＪＰ，Ａ) 特開 昭55−134107（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) B23B 27/14 B23P 15/28 C22C 29/02 C22C 29/08 C23C 14/06 C23C 16/30 Continued on the front page (51) Int.Cl. 7 Identification symbol FI C23C 16/30 C23C 16/30 (72) Inventor ▲ Isao Toshi 1511 Furamagi, Ishishita-cho, Yuki-gun, Ibaraki Prefecture Mitsubishi Materials Corporation Tsukuba Works (72) Inventor Yuki Hamaguchi 1511 Furamagi, Ishishita-cho, Yuki-gun, Ibaraki Prefecture Mitsubishi Materials Corporation Tsukuba Works Examiner Koji Manaka (56) References JP-A 7-180071 (JP, A) JP-A Sho 63-114970 (JP, A) JP-A-55-134107 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) B23B 27/14 B23P 15/28 C22C 29/02 C22C 29 / 08 C23C 14/06 C23C 16/30
Claims (2)
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。1. 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
one or more of i, Nb, and Cr), and / or both: 5 to 30% by weight of the solid dispersion and the carbonitride solid solution. 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 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 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.
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。2. 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
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. ~ 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 JPH1142504A (en) | 1999-02-16 |
| JP3331916B2 true 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) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5561522B2 (en) * | 2010-02-26 | 2014-07-30 | 三菱マテリアル株式会社 | Surface-coated WC-based cemented carbide insert |
| JP5613888B2 (en) * | 2010-05-07 | 2014-10-29 | 三菱マテリアル株式会社 | Surface-coated WC-based cemented carbide insert |
-
1997
- 1997-07-29 JP JP20310997A patent/JP3331916B2/en not_active Ceased
Also Published As
| Publication number | Publication date |
|---|---|
| JPH1142504A (en) | 1999-02-16 |
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