JP2005262323A - Surface-coated cermet cutting tool with hard coating layer having excellent chipping resistance - Google Patents
Surface-coated cermet cutting tool with hard coating layer having excellent chipping resistance Download PDFInfo
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Abstract
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この発明は、特に鋼や鋳鉄などの高速断続切削加工で、硬質被覆層がすぐれた耐チッピング性を発揮する表面被覆サーメット製切削工具（以下、被覆サーメット工具という）に関するものである。 The present invention relates to a surface-coated cermet cutting tool (hereinafter referred to as a coated cermet tool) that exhibits excellent chipping resistance with a hard coating layer, particularly in high-speed intermittent cutting of steel or cast iron.
従来、一般に、炭化タングステン（以下、ＷＣで示す）基超硬合金または炭窒化チタン（以下、ＴｉＣＮで示す）基サーメットで構成された基体（以下、これらを総称して工具基体という）の表面に、
（ａ）下部層として、いずれも化学蒸着形成されたＴｉの炭化物（以下、ＴｉＣで示す）層、窒化物（以下、同じく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、および炭窒酸化物（以下、ＴｉＣＮＯで示す）層のうちの１層または２層以上からなり、かつ３〜２０μｍの合計平均層厚を有するＴｉ化合物層、
（ｂ）上部層として、化学蒸着形成した状態でα型の結晶構造を有し、かつ１〜１５μｍの平均層厚を有する蒸着α型酸化アルミニウム（以下、Ａｌ2Ｏ3で示す）層、
以上（ａ）および（ｂ）で構成された硬質被覆層を形成してなる被覆サーメット工具が知られており、この被覆サーメット工具が、例えば各種の鋼や鋳鉄などの連続切削や断続切削に用いられていることも知られている。
Conventionally, generally on the surface of a substrate (hereinafter collectively referred to as a tool substrate) composed of a tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet. ,
(A) As a lower layer, a Ti carbide (hereinafter referred to as TiC) layer, nitride (hereinafter also referred to as TiN) layer, carbonitride (hereinafter referred to as TiCN) layer formed by chemical vapor deposition, Ti compound layer comprising one or more of a carbon oxide (hereinafter referred to as TiCO) layer and a carbonitride oxide (hereinafter referred to as TiCNO) layer and having a total average layer thickness of 3 to 20 μm ,
(B) a vapor-deposited α-type aluminum oxide (hereinafter referred to as Al 2 O 3 ) layer having an α-type crystal structure in the state of chemical vapor deposition and having an average layer thickness of 1 to 15 μm as an upper layer;
A coated cermet tool formed by forming a hard coating layer composed of (a) and (b) above is known, and this coated cermet tool is used for continuous cutting and intermittent cutting of various steels and cast irons, for example. It is also known that
また、一般に、上記の被覆サーメット工具の硬質被覆層を構成するＴｉ化合物層や蒸着α型Ａｌ2 Ｏ3 層が粒状結晶組織を有し、さらに、前記Ｔｉ化合物層を構成するＴｉＣＮ層を、層自身の強度向上を目的として、通常の化学蒸着装置にて、反応ガスとして有機炭窒化物、例えばＣＨ3ＣＮを含む混合ガスを使用し、７００〜９５０℃の中温温度域で化学蒸着することにより形成して縦長成長結晶組織をもつようにすることも知られている。
近年の切削装置の高性能化はめざましく、一方で切削加工に対する省力化および省エネ化、さらに低コスト化の要求は強く、これに伴い、切削加工は一段と高速化の傾向にあるが、上記の従来被覆サーメット工具においては、これを鋼や鋳鉄などの通常の条件での連続切削や断続切削に用いた場合には問題はないが、特にこれを切削条件の最も厳しい高速断続切削、すなわち切刃部にきわめて短いピッチで繰り返し機械的熱的衝撃の加わる高速断続切削に用いた場合、硬質被覆層の下部層であるＴｉ化合物層は高強度を有し、すぐれた耐チッピング性を示すものの、同上部層を構成する蒸着α型Ａｌ2Ｏ3層は、硬質で耐熱性にすぐれるものの、機械的熱的衝撃に対してきわめて脆いものであるために、これが原因で硬質被覆層にはチッピング（微小欠け）が発生し易くなり、この結果比較的短時間で使用寿命に至るのが現状である。 In recent years, the performance of cutting machines has been remarkable. On the other hand, there is a strong demand for labor saving, energy saving, and cost reduction for cutting, and along with this, cutting has been on the trend of higher speed. For coated cermet tools, there is no problem when this is used for continuous cutting and interrupted cutting under normal conditions such as steel and cast iron. The Ti compound layer, which is the lower layer of the hard coating layer, has high strength and excellent chipping resistance when used for high-speed interrupted cutting with repeated mechanical thermal shock at a very short pitch. The vapor-deposited α-type Al 2 O 3 layer that makes up the layer is hard and has excellent heat resistance, but it is extremely brittle to mechanical thermal shocks. (Slight chipping) is likely to occur, and as a result, the service life is reached in a relatively short time.
そこで、本発明者等は、上述のような観点から、上記の被覆サーメット工具の硬質被覆層の上部層を構成する蒸着α型Ａｌ2Ｏ3層の耐チッピング性向上をはかるべく研究を行った結果、
工具基体の表面に、通常の化学蒸着装置で、下部層として、通常の条件で、上記Ｔｉ化合物層を形成した後、同じく通常の条件で、κ型またはθ型の結晶構造を有し、かつ、
組成式：（Ａｌ１−Ｘ ＺｒＸ ）2 Ｏ3 、
で現した場合、電子線マイクロアナライザー（ＥＰＭＡ）で測定して、Ｘ値が０．００３〜０．０５を満足するＡｌ系酸化物［以下、（Ａｌ，Ｚｒ）2 Ｏ3 で示す］層を蒸着形成し、ついで、前記（Ａｌ，Ｚｒ）2 Ｏ3 層の表面を、同じく化学蒸着装置にて、
反応ガス組成：体積％で、ＴｉＣｌ４：０．２〜３％、ＣＯ２：０．２〜１０％、Ａｒ：５〜５０％、Ｈ２：残り、
反応雰囲気温度：９００〜１０２０℃、
反応雰囲気圧力：７〜３０ｋＰａ、
時間：１〜１０分、
の条件で処理すると、前記（Ａｌ，Ｚｒ）2 Ｏ3 層の表面には、
組成式：ＴｉＯＹ 、
で表わした場合、オージェ分光分析装置で測定して、Ｙ値がＴｉに対する原子比で１．２〜１．９、を満足するＴｉ酸化物微粒が分散分布するようになり、この状態で、加熱処理、望ましくは圧力：７〜５０ｋＰａのＡｒ雰囲気中、温度：１０００〜１２００℃に１０〜１２０分間保持の条件で加熱処理を施して、前記κ型またはθ型の結晶構造の（Ａｌ，Ｚｒ）2 Ｏ3 層をα型結晶構造の（Ａｌ，Ｚｒ）2 Ｏ3 層に変態させると、この結果の加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層においては、前記変態前の（Ａｌ，Ｚｒ）2 Ｏ3 層の表面に一様に分散分布したＴｉ酸化物微粒が前記κ型またはθ型の結晶構造からα型結晶構造へ変態する際に発生する割れ（クラック）の起点となることから、変態発生割れはきわめて微細化し、かつ一様に分散分布した状態となると共に、構成成分であるＺｒの作用で前記（Ａｌ，Ｚｒ）2 Ｏ3 層自体の強度が著しく向上したものになることから、この結果形成された加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層は、変態発生割れが層全体に亘って微細にして、均一化された組織を有し、かつ高強度を有するようになり、機械的熱的衝撃に対してきわめて強固なものとなり、すぐれた耐チッピング性を具備するようになり、したがって、硬質被覆層の上部層が前記加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層、下部層が上記Ｔｉ化合物層（このＴｉ化合物層には上記の条件での加熱処理では何らの変化も起らない）で構成された被覆サーメット工具は、特に激しい機械的熱的衝撃を伴なう高速断続切削加工でも、前記加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層が、α型Ａｌ2 Ｏ3 層の本来具備するすぐれた高温硬さおよび耐熱性と同等の高温硬さと耐熱性を具備した状態で、すぐれた耐チッピング性を発揮することから、高強度を有する前記Ｔｉ化合物層の共存と相俟って、硬質被覆層におけるチッピング発生が著しく抑制され、長期に亘ってすぐれた耐摩耗性を示すようになるという研究結果を得たのである。
In view of the above, the present inventors have conducted research to improve the chipping resistance of the vapor-deposited α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer of the above coated cermet tool. result,
On the surface of the tool base, after forming the Ti compound layer under normal conditions as a lower layer with a normal chemical vapor deposition apparatus, it has a κ-type or θ-type crystal structure under the same normal conditions, and ,
Composition formula: (Al 1-X Zr X ) 2 O 3,
In this case, an Al-based oxide [hereinafter referred to as (Al, Zr) 2 O 3 ] layer satisfying an X value of 0.003 to 0.05 is measured by an electron beam microanalyzer (EPMA). Then, the surface of the (Al, Zr) 2 O 3 layer is formed by the same chemical vapor deposition apparatus.
Reaction gas composition: by volume%, TiCl 4: 0.2~3%, CO 2: 0.2~10%, Ar: 5~50%, H 2: remainder,
Reaction atmosphere temperature: 900-1020 ° C.
Reaction atmosphere pressure: 7-30 kPa,
Time: 1-10 minutes
When the treatment is performed under the conditions, the surface of the (Al, Zr) 2 O 3 layer is
Composition formula: TiO Y ,
In this state, Ti oxide fine particles satisfying a Y value of 1.2 to 1.9 in terms of atomic ratio to Ti as measured by an Auger spectroscopic analyzer are dispersed and distributed. Treatment, preferably heat treatment in an Ar atmosphere at a pressure of 7 to 50 kPa, and a temperature of 1000 to 1200 ° C. for 10 to 120 minutes, so that the κ-type or θ-type crystal structure (Al, Zr) (Al, Zr) of the 2 O 3 layer α-type crystal structure when is transformed into 2 O 3 layer, as a result of heating transformation α-type (Al, Zr) in 2 O 3 layer, the transformation before (Al, Zr) The origin of cracks that occur when the Ti oxide fine particles uniformly distributed on the surface of the 2 O 3 layer are transformed from the κ-type or θ-type crystal structure to the α-type crystal structure. Therefore, transformation cracks are extremely fine and distributed uniformly In addition, the strength of the (Al, Zr) 2 O 3 layer itself is remarkably improved by the action of Zr as a constituent component, so that the resulting heat-transformed α-type (Al, Zr) ) The 2 O 3 layer has transformation cracks that are made fine throughout the layer, has a uniform structure, and has high strength, and is extremely strong against mechanical and thermal shock. Therefore, it has excellent chipping resistance. Therefore, the upper layer of the hard coating layer is the heat-transformed α-type (Al, Zr) 2 O 3 layer, and the lower layer is the Ti compound layer (this Ti compound layer). The coated cermet tool constituted by the heat treatment under the above-described conditions does not cause any change even in the high-speed interrupted cutting process accompanied by severe mechanical thermal shock. Al, Zr) 2 O 3 layers, alpha-type Al 2 O 3 Since it exhibits excellent chipping resistance in the state of having high temperature hardness and heat resistance equivalent to the original high temperature hardness and heat resistance, the coexistence and coexistence of the Ti compound layer having high strength Thus, the research results have been obtained that the occurrence of chipping in the hard coating layer is remarkably suppressed, and excellent wear resistance is exhibited over a long period of time.
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、ＷＣ基超硬合金またはＴｉＣＮ基サーメットで構成された工具基体の表面に、
（ａ）下部層として、いずれも化学蒸着形成されたＴｉＣ層、ＴｉＮ層、ＴｉＣＮ層、ＴｉＣＯ層、およびＴｉＣＮＯ層のうちの１層または２層以上からなり、かつ３〜２０μｍの合計平均層厚を有するＴｉ化合物層、
（ｂ）上部層として、化学蒸着形成した状態でκ型またはθ型の結晶構造を有し、かつ、
組成式：（Ａｌ１−Ｘ ＺｒＸ ）2 Ｏ3 、
で表わした場合、電子線マイクロアナライザー（ＥＰＭＡ）で測定して、Ｘ値が原子比で０．００３〜０．０５を満足する（Ａｌ，Ｚｒ）2 Ｏ3 層の表面に、
変態発生割れ起点材として、化学蒸着形成され、かつ、
組成式：ＴｉＯＹ 、
で表わした場合、オージェ分光分析装置で測定して、Ｙ値がＴｉに対する原子比で１．２〜１．９、を満足するＴｉ酸化物微粒を分散分布させた状態で、加熱処理を施して、前記κ型またはθ型の結晶構造を有する（Ａｌ，Ｚｒ）2 Ｏ3 層の結晶構造をα型結晶構造に変態してなると共に、１〜１５μｍの平均層厚を有する加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層、
以上（ａ）および（ｂ）で構成された硬質被覆層を形成してなる、硬質被覆層がすぐれた耐チッピング性を発揮する被覆サーメット工具に特徴を有するものである。
The present invention has been made based on the above research results, and on the surface of a tool base composed of a WC-based cemented carbide or TiCN-based cermet,
(A) The lower layer is composed of one or more of TiC layer, TiN layer, TiCN layer, TiCO layer, and TiCNO layer formed by chemical vapor deposition, and has a total average layer thickness of 3 to 20 μm. A Ti compound layer having
(B) the upper layer has a κ-type or θ-type crystal structure in the state of chemical vapor deposition, and
Composition formula: (Al 1-X Zr X ) 2 O 3,
In the surface of the (Al, Zr) 2 O 3 layer, which is measured by an electron beam microanalyzer (EPMA) and the X value satisfies the atomic ratio of 0.003 to 0.05,
As a transformation initiation crack starting material, chemical vapor deposition is formed, and
Composition formula: TiO Y ,
In the state in which Ti oxide fine particles satisfying a Y value of 1.2 to 1.9 in terms of atomic ratio to Ti are dispersed and distributed as measured with an Auger spectroscopic analyzer, heat treatment is performed. The heat-transformed α-type having an average layer thickness of 1 to 15 μm as well as the crystal structure of the (Al, Zr) 2 O 3 layer having the κ-type or θ-type crystal structure being transformed into an α-type crystal structure ( Al, Zr) 2 O 3 layer,
The hard coating layer formed by the hard coating layer configured as described above in (a) and (b) is characterized by a coated cermet tool that exhibits excellent chipping resistance.
つぎに、この発明の被覆サーメット工具の硬質被覆層の構成層について、上記の通りに数値限定した理由を以下に説明する。
（ａ）下部層（Ｔｉ化合物層）の平均層厚
Ｔｉ化合物層は、自体が高強度を有し、これの存在によって硬質被覆層が高強度を具備するようになるほか、工具基体と上部層である加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層のいずれにも強固に密着し、よって硬質被覆層の工具基体に対する密着性向上に寄与する作用をもつが、その合計平均層厚が３μｍ未満では、前記作用を十分に発揮させることができず、一方その合計平均層厚が２０μｍを越えると、特に高熱発生を伴なう高速断続切削で熱塑性変形を起し易くなり、これが偏摩耗の原因となることから、その合計平均層厚を３〜２０μｍと定めた。
（ｂ）Ｔｉ酸化物微粒のＹ値
Ｔｉ酸化物微粒は、上記の通り蒸着κ型またはθ型（Ａｌ，Ｚｒ）2 Ｏ3 層のα型（Ａｌ，Ｚｒ）2 Ｏ3 層への加熱変態時に発生する割れの起点となることから、加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層における変態発生割れは、微細化し、かつ一様に分散分布したものとなり、この結果前記加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層はすぐれた耐チッピング性を具備するようになるが、そのＹ値がＴｉに対する原子比で１．２未満でも、また同１．９を越えても変態発生割れ微細化効果を十分に発揮させることができなくなることから、そのＹ値をＴｉに対する原子比で１．２〜１．９と定めた。
（ｃ）上部層［加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層］のＺｒの含有割合および平均層厚
加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層は、構成成分であるＡｌの作用ですぐれた高温硬さと耐熱性を有し、かつ同Ｚｒの作用で高強度を有することから、すぐれた耐摩耗性と耐チッピング性を発揮するようになるが、Ｚｒの含有割合（Ｘ値）が、Ａｌとの合量に占める割合で、原子比で（以下同じ）０．００３未満では、十分な強度向上効果を発揮することができず、一方Ｚｒの含有割合が同０．０５を越えると変態に乱れが生じ、加熱処理でのκ型またはθ型結晶構造からα型結晶構造への変態を満足に行うことが困難になることから、Ｚｒの含有割合（Ｘ値）を０．００３〜０．０５と定めた。
Next, the reason why the constituent layers of the hard coating layer of the coated cermet tool of the present invention are numerically limited as described above will be described below.
(A) Average layer thickness of lower layer (Ti compound layer) The Ti compound layer itself has high strength, and the presence of the Ti compound layer makes the hard coating layer have high strength, and the tool base and upper layer. The heat-transformed α-type (Al, Zr) 2 O 3 layer is firmly adhered to each other, and thus has an effect of improving the adhesion of the hard coating layer to the tool substrate, but the total average layer thickness is 3 μm. If the total thickness is less than 20 μm, thermoplastic deformation is likely to occur particularly in high-speed intermittent cutting with high heat generation, which causes uneven wear. Since it becomes a cause, the total average layer thickness was determined as 3-20 micrometers.
(B) Y value of Ti oxide fine particles Ti oxide fine particles are formed by heating transformation of vapor deposition κ-type or θ-type (Al, Zr) 2 O 3 layer to α-type (Al, Zr) 2 O 3 layer as described above. Since this is the starting point of cracks that sometimes occur, transformation cracks in the heat-transformed α-type (Al, Zr) 2 O 3 layer are refined and uniformly distributed. As a result, the heat-transformed α-type The (Al, Zr) 2 O 3 layer has excellent chipping resistance. However, even if the Y value is less than 1.2 or more than 1.9 in terms of atomic ratio to Ti, transformation cracking occurs. The Y value was determined to be 1.2 to 1.9 in terms of the atomic ratio with respect to Ti because the effect of miniaturization could not be sufficiently exhibited.
(C) Zr content and average layer thickness of upper layer [heat-transformed α-type (Al, Zr) 2 O 3 layer] The heat-transformed α-type (Al, Zr) 2 O 3 layer is composed of the constituent Al It has excellent high temperature hardness and heat resistance due to its action, and high strength due to the action of the same Zr, so that it exhibits excellent wear resistance and chipping resistance, but the Zr content ratio (X value ) Is a proportion of the total amount of Al, and if the atomic ratio is less than 0.003 (the same shall apply hereinafter), sufficient strength improvement effect cannot be exhibited, while the Zr content is 0.05. If this is exceeded, the transformation will be disturbed, and it will be difficult to satisfactorily transform from the κ-type or θ-type crystal structure to the α-type crystal structure in the heat treatment. 003 to 0.05.
また、加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層の平均層厚が１μｍ未満では、硬質被覆層に十分な高温硬さと耐熱性を具備せしめることができず、一方その平均層厚が１５μｍを越えて厚くなりすぎると、チッピングが発生し易くなることから、その平均層厚を１〜１５μｍと定めた。 If the average thickness of the heat-transformed α-type (Al, Zr) 2 O 3 layer is less than 1 μm, the hard coating layer cannot be provided with sufficient high-temperature hardness and heat resistance, while the average layer thickness is 15 μm. If the thickness is too thick, chipping is likely to occur. Therefore, the average layer thickness is set to 1 to 15 μm.
なお、切削工具の使用前後の識別を目的として、黄金色の色調を有するＴｉＮ層を、必要に応じて蒸着形成してもよいが、この場合の平均層厚は０．１〜１μｍでよく、これは０．１μｍ未満では、十分な識別効果が得られず、一方前記ＴｉＮ層による前記識別効果は１μｍまでの平均層厚で十分であるという理由からである。 In addition, for the purpose of identification before and after the use of the cutting tool, a TiN layer having a golden color tone may be vapor-deposited as necessary, but the average layer thickness in this case may be 0.1 to 1 μm, This is because if the thickness is less than 0.1 μm, a sufficient discrimination effect cannot be obtained, while the discrimination effect by the TiN layer is sufficient with an average layer thickness of up to 1 μm.
この発明被覆サーメット工具は、機械的熱的衝撃がきわめて高い鋼や鋳鉄などの高速断続切削でも、硬質被覆層の上部層を構成する加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層がすぐれた高温硬さと耐熱性、さらにすぐれた耐チッピング性を発揮することから、硬質被覆層にチッピングの発生なく、すぐれた耐摩耗性を示すものである。 The coated cermet tool of the present invention has an excellent heat-transformed α-type (Al, Zr) 2 O 3 layer that constitutes the upper layer of the hard coating layer even in high-speed intermittent cutting such as steel and cast iron with extremely high mechanical and thermal shock. Since it exhibits high temperature hardness and heat resistance, and excellent chipping resistance, the hard coating layer exhibits excellent wear resistance without occurrence of chipping.
つぎに、この発明の被覆サーメット工具を実施例により具体的に説明する。 Next, the coated cermet tool of the present invention will be specifically described with reference to examples.
原料粉末として、いずれも１〜３μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＶＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ3 Ｃ2 粉末、ＴｉＮ粉末、ＴａＮ粉末、およびＣｏ粉末を用意し、これら原料粉末を、表１に示される配合組成に配合し、さらにワックスを加えてアセトン中で２４時間ボールミル混合し、減圧乾燥した後、９８ＭＰａの圧力で所定形状の圧粉体にプレス成形し、この圧粉体を５Ｐａの真空中、１３７０〜１４７０℃の範囲内の所定の温度に１時間保持の条件で真空焼結し、焼結後、切刃部にＲ：０．０７ｍｍのホーニング加工を施すことによりＩＳＯ・ＣＮＭＧ１２０４０８に規定するスローアウエイチップ形状をもったＷＣ基超硬合金製の工具基体Ａ〜Ｆをそれぞれ製造した。 WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, TaN powder, and Co powder all having an average particle diameter of 1 to 3 μm are prepared as raw material powders. These raw material powders were blended into the composition shown in Table 1, added with wax, ball milled in acetone for 24 hours, dried under reduced pressure, and pressed into a green compact with a predetermined shape at a pressure of 98 MPa. The green compact was vacuum sintered at a predetermined temperature in the range of 1370 to 1470 ° C. for 1 hour in a vacuum of 5 Pa. After sintering, the cutting edge portion was R: 0.07 mm honing By performing the processing, tool bases A to F made of a WC-base cemented carbide having a throwaway tip shape specified in ISO · CNMG120408 were manufactured.
また、原料粉末として、いずれも０．５〜２μｍの平均粒径を有するＴｉＣＮ（質量比でＴｉＣ／ＴｉＮ＝５０／５０）粉末、Ｍｏ2 Ｃ粉末、ＺｒＣ粉末、ＮｂＣ粉末、ＴａＣ粉末、ＷＣ粉末、Ｃｏ粉末、およびＮｉ粉末を用意し、これら原料粉末を、表２に示される配合組成に配合し、ボールミルで２４時間湿式混合し、乾燥した後、９８ＭＰａの圧力で圧粉体にプレス成形し、この圧粉体を１．３ｋＰａの窒素雰囲気中、温度：１５４０℃に１時間保持の条件で焼結し、焼結後、切刃部分にＲ：０．０７ｍｍのホーニング加工を施すことによりＩＳＯ規格・ＣＮＭＧ１２０４１２のチップ形状をもったＴｉＣＮ基サーメット製の工具基体ａ〜ｆを形成した。 In addition, as raw material powders, TiCN (mass ratio TiC / TiN = 50/50) powder, Mo 2 C powder, ZrC powder, NbC powder, TaC powder, WC powder, all having an average particle diameter of 0.5 to 2 μm. Co powder and Ni powder are prepared, and these raw material powders are blended in the blending composition shown in Table 2, wet mixed by a ball mill for 24 hours, dried, and pressed into a compact at a pressure of 98 MPa. The green compact was sintered in a nitrogen atmosphere of 1.3 kPa at a temperature of 1540 ° C. for 1 hour, and after the sintering, the cutting edge portion was subjected to a honing process of R: 0.07 mm. Tool bases a to f made of TiCN-based cermet having a standard / CNMG12041 chip shape were formed.
つぎに、これらの工具基体Ａ〜Ｆおよび工具基体ａ〜ｆの表面に、通常の化学蒸着装置を用い、表３（表３中のｌ−ＴｉＣＮは特開平６−８０１０号公報に記載される縦長成長結晶組織をもつＴｉＣＮ層の形成条件を示すものであり、これ以外は通常の粒状結晶組織の形成条件を示すものである）に示される条件にて、硬質被覆層の下部層としてＴｉ化合物層を、表５に示される組み合わせで、かつ目標層厚で蒸着形成し、ついで同じく表３に示される条件にて、結晶構造がκ型またはθ型の（Ａｌ，Ｚｒ）2 Ｏ3 層を同じく表５に示される組み合わせで、かつ目標層厚で蒸着形成し、ついで前記κ型またはθ型の（Ａｌ，Ｚｒ）2 Ｏ3 層の表面に、Ｔｉ酸化物微粒を同じく表４に示される条件で表５に示される組み合わせで蒸着形成した状態で、これに３０ｋＰａのＡｒ雰囲気中、温度：１１００℃に２０〜１００分の範囲内の所定の時間保持の条件で加熱処理を施して、前記κ型またはθ型の結晶構造の（Ａｌ，Ｚｒ）2 Ｏ3 層をα型結晶構造の（Ａｌ，Ｚｒ）2 Ｏ3 層に変態させてなる加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層を硬質被覆層の上部層として形成することにより本発明被覆サーメット工具１〜１３をそれぞれ製造した。 Next, an ordinary chemical vapor deposition apparatus is used on the surfaces of the tool bases A to F and the tool bases a to f, and Table 3 (l-TiCN in Table 3 is described in JP-A-6-8010). Ti compound as a lower layer of the hard coating layer under the conditions shown in (1) shows the conditions for forming a TiCN layer having a vertically grown crystal structure, and (2) shows conditions for forming a normal granular crystal structure. The layers are formed by vapor deposition in the combinations shown in Table 5 and with the target layer thickness, and then the (Al, Zr) 2 O 3 layer having a crystal structure of κ type or θ type is formed under the same conditions shown in Table 3. Similarly, the deposition shown in Table 5 is performed with the target layer thickness, and then Ti oxide fine particles are also shown in Table 4 on the surface of the κ-type or θ-type (Al, Zr) 2 O 3 layer. In a state where vapor deposition is formed in the combination shown in Table 5 under conditions In an Ar atmosphere at 30kPa thereto, temperature: 1100 ° C. and subjected to heat treatment at a predetermined time holding conditions in the range of 20 to 100 minutes, the κ-type or θ-type crystal structure (Al, Zr) 2 By forming the heat-transformed α-type (Al, Zr) 2 O 3 layer as an upper layer of the hard coating layer by transforming the O 3 layer into an (Al, Zr) 2 O 3 layer having an α-type crystal structure, the present invention Coated cermet tools 1 to 13 were produced.
なお、上記本発明被覆サーメット工具１〜１３の製造に際しては、それぞれ別途試験片を用意し、この試験片を同じく化学蒸着装置に装入し、前記試験片の表面にＴｉ酸化物微粒が形成された時点で装置から取りだし、前記Ｔｉ酸化物微粒の組成（Ｙ値）をオージェ分光分析装置で測定した。 In the production of the cermet tools 1 to 13 according to the present invention, a separate test piece is prepared, and the test piece is loaded into the chemical vapor deposition apparatus, and Ti oxide fine particles are formed on the surface of the test piece. At that time, it was taken out from the apparatus, and the composition (Y value) of the Ti oxide fine particles was measured with an Auger spectroscopic analyzer.
また、比較の目的で、表６に示される通り、硬質被覆層の上部層として同じく表３に示される条件で、同じく表６に示される目標層厚の蒸着α型Ａｌ2Ｏ3層を形成し、かつ上記のＴｉ酸化物微粒の形成および上記条件での加熱処理を行わない以外は同一の条件で従来被覆サーメット工具１〜１３をそれぞれ製造した。 For comparison purposes, as shown in Table 6, an evaporated α-type Al 2 O 3 layer having the target layer thickness shown in Table 6 is also formed as the upper layer of the hard coating layer under the same conditions as shown in Table 3. And conventionally the coated cermet tools 1-13 were each manufactured on the same conditions except not performing formation of said Ti oxide fine particle, and heat processing on the said conditions.
この結果得られた本発明被覆サーメット工具１〜１３および従来被覆サーメット工具１〜１３について、これの硬質被覆層の構成層を電子線マイクロアナライザー（ＥＰＭＡ）およびオージェ分光分析装置を用いて観察（層の縦断面を観察）したところ、前者ではいずれも目標組成と実質的に同じ組成を有するＴｉ化合物層と加熱変態α型（Ａｌ，Ｚｒ）2 Ｏ3 層からなり、かつ表面部に加熱処理前に蒸着されたＴｉ酸化物微粒も上記の測定で目標組成と実質的に同じ組成を示すものであった。一方後者でも、いずれも同じく目標組成と実質的に同じ組成を有するＴｉ化合物と蒸着α型Ａｌ2Ｏ3層からなることが確認された。さらに、これらの被覆サーメット工具の硬質被覆層の構成層の厚さを、走査型電子顕微鏡を用いて測定（同じく縦断面測定）したところ、いずれも目標層厚と実質的に同じ平均層厚（５点測定の平均値）を示した。 For the obtained coated cermet tools 1 to 13 and the conventional coated cermet tools 1 to 13 obtained as a result, the constituent layers of the hard coating layer were observed using an electron beam microanalyzer (EPMA) and an Auger spectroscopic analyzer (layers). In the former case, the former consists of a Ti compound layer having substantially the same composition as the target composition and a heat-transformed α-type (Al, Zr) 2 O 3 layer, and the surface portion is subjected to heat treatment. The Ti oxide fine particles deposited on the substrate also showed substantially the same composition as the target composition in the above measurement. On the other hand, it was confirmed that both of the latter consisted of a Ti compound having substantially the same composition as the target composition and a deposited α-type Al 2 O 3 layer. Furthermore, when the thickness of the constituent layer of the hard coating layer of these coated cermet tools was measured using a scanning electron microscope (similarly longitudinal section measurement), the average layer thickness was substantially the same as the target layer thickness ( Average value of 5-point measurement) was shown.
つぎに、上記の各種の被覆サーメット工具をいずれも工具鋼製バイトの先端部に固定治具にてネジ止めした状態で、本発明被覆サーメット工具１〜１３および従来被覆サーメット工具１〜１３について、
被削材：ＪＩＳ・ＳＵＪ２の長さ方向等間隔４本縦溝入り丸棒、
切削速度：３５０ｍ／ｍｉｎ、
切り込み：１．５ｍｍ、
送り：０．２０ｍｍ／ｒｅｖ、
切削時間：５分、
の条件（切削条件Ａという）でのベアリング鋼の乾式高速断続切削試験（通常の切削速度は２００ｍ／ｍｉｎ）、
被削材：ＪＩＳ・ＳＣＭ４４０の長さ方向等間隔４本縦溝入り丸棒、
切削速度：４００ｍ／ｍｉｎ、
切り込み：１．５ｍｍ、
送り：０．２２ｍｍ／ｒｅｖ、
切削時間：５分、
の条件（切削条件Ｂという）での合金鋼の乾式高速断続切削試験（通常の切削速度は２００ｍ／ｍｉｎ）、
被削材：ＪＩＳ・ＦＣＤ４００の長さ方向等間隔４本縦溝入り丸棒、
切削速度：４００ｍ／ｍｉｎ、
切り込み：２．０ｍｍ、
送り：０．３０ｍｍ／ｒｅｖ、
切削時間：５分、
の条件（切削条件Ｃという）でのダクタイル鋳鉄の乾式高速断続切削試験（通常の切削速度は２００ｍ／ｍｉｎ）を行い、いずれの切削試験でも切刃の逃げ面摩耗幅を測定した。この測定結果を表７に示した。
Next, in the state where each of the various coated cermet tools is screwed to the tip of the tool steel tool with a fixing jig, the present coated cermet tools 1 to 13 and the conventional coated cermet tools 1 to 13 are as follows.
Work material: JIS / SUJ2 lengthwise equidistant four round grooved round bars,
Cutting speed: 350 m / min,
Incision: 1.5mm,
Feed: 0.20mm / rev,
Cutting time: 5 minutes
Dry high-speed intermittent cutting test (normal cutting speed is 200 m / min) of bearing steel under the conditions (referred to as cutting condition A),
Work material: JIS · SCM440 lengthwise equidistant 4 vertical grooved round bar,
Cutting speed: 400 m / min,
Incision: 1.5mm,
Feed: 0.22mm / rev,
Cutting time: 5 minutes
Dry high-speed intermittent cutting test (normal cutting speed is 200 m / min) of alloy steel under the above conditions (referred to as cutting condition B),
Work material: JIS / FCD400 in the longitudinal direction, 4 equally spaced round bars,
Cutting speed: 400 m / min,
Cutting depth: 2.0 mm,
Feed: 0.30mm / rev,
Cutting time: 5 minutes
A dry high-speed intermittent cutting test (normal cutting speed is 200 m / min) of ductile cast iron under the above conditions (referred to as cutting condition C), and the flank wear width of the cutting edge was measured in any cutting test. The measurement results are shown in Table 7.
上述のように、この発明の被覆サーメット工具は、各種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、特に厳しい切削条件となる高速断続切削でもすぐれた耐チッピング性を示し、長期に亘ってすぐれた切削性能を発揮するものであるから、切削装置の高性能化並びに切削加工の省力化および省エネ化、さらに低コスト化に十分満足に対応できるものである。 As described above, the coated cermet tool of the present invention has excellent chipping resistance not only in continuous cutting and intermittent cutting under normal conditions such as various steels and cast iron, but also in high-speed intermittent cutting which is particularly severe cutting conditions. Since it exhibits excellent cutting performance over a long period of time, it can sufficiently satisfy the high performance of the cutting device, the labor saving and energy saving of the cutting work, and the cost reduction.
Claims (1)
（ａ）下部層として、いずれも化学蒸着形成されたＴｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、および炭窒酸化物層のうちの１層または２層以上からなり、かつ３〜２０μｍの合計平均層厚を有するＴｉ化合物層、
（ｂ）上部層として、化学蒸着形成した状態でκ型またはθ型の結晶構造を有し、かつ、
組成式：（Ａｌ１−Ｘ ＺｒＸ ）2 Ｏ3 、
で表わした場合、電子線マイクロアナライザー（ＥＰＭＡ）で測定して、Ｘ値が原子比で０．００３〜０．０５を満足するＡｌ系酸化物層の表面に、
変態発生割れ起点材として、化学蒸着形成され、かつ、
組成式：ＴｉＯＹ 、
で表わした場合、オージェ分光分析装置で測定して、Ｙ値がＴｉに対する原子比で１．２〜１．９、を満足するＴｉ酸化物微粒を分散分布させた状態で、加熱処理を施して、前記κ型またはθ型の結晶構造を有するＡｌ系酸化物層の結晶構造をα型結晶構造に変態してなると共に、１〜１５μｍの平均層厚を有する加熱変態α型Ａｌ系酸化物層、
以上（ａ）および（ｂ）で構成された硬質被覆層を形成してなる硬質被覆層がすぐれた耐チッピング性を発揮する表面被覆サーメット製切削工具。 On the surface of the tool base composed of tungsten carbide based cemented carbide or titanium carbonitride based cermet,
(A) As a lower layer, each consists of one or two or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer, and carbonitride oxide layer formed by chemical vapor deposition, And a Ti compound layer having a total average layer thickness of 3 to 20 μm,
(B) the upper layer has a κ-type or θ-type crystal structure in the state of chemical vapor deposition, and
Composition formula: (Al 1-X Zr X ) 2 O 3,
When measured by an electron beam microanalyzer (EPMA), the surface of the Al-based oxide layer satisfying an X value of 0.003 to 0.05 by atomic ratio,
As a transformation initiation crack starting material, chemical vapor deposition is formed, and
Composition formula: TiO Y ,
In the state in which Ti oxide fine particles satisfying a Y value of 1.2 to 1.9 in terms of atomic ratio to Ti are dispersed and distributed as measured with an Auger spectroscopic analyzer, heat treatment is performed. The heat-transformed α-type Al-based oxide layer having an average layer thickness of 1 to 15 μm, wherein the crystal structure of the Al-based oxide layer having the κ-type or θ-type crystal structure is transformed into an α-type crystal structure ,
A surface-coated cermet cutting tool in which the hard coating layer formed by the hard coating layer constituted of (a) and (b) exhibits excellent chipping resistance.
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| Application Number | Priority Date | Filing Date | Title |
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| JP2004058682A JP4210930B2 (en) | 2004-02-18 | 2004-03-03 | Surface-coated throw-away tip that exhibits excellent chipping resistance with a hard coating layer in high-speed intermittent cutting |
| DE602004031919T DE602004031919D1 (en) | 2003-12-22 | 2004-12-21 | Coated cermet hard-coated cutting tool with excellent impact resistance. |
| CNB200410095404XA CN100445023C (en) | 2003-12-22 | 2004-12-21 | Surface-coated cermet cutting tool with hard coating layer having excellend chipping resistance |
| AT04106794T ATE503038T1 (en) | 2003-12-22 | 2004-12-21 | COATED CERMET CUTTING TOOL WITH HARD COATING LAYER WITH EXCELLENT IMPACT RESISTANCE. |
| EP04106794A EP1548154B1 (en) | 2003-12-22 | 2004-12-21 | Surface-coated cermet cutting tool with hard coating layer having excellent chipping resistance |
| US11/019,656 US7273665B2 (en) | 2003-12-22 | 2004-12-21 | Surface-coated cermet cutting tool with hard coating layer having excellent chipping resistance |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008093769A (en) * | 2006-10-10 | 2008-04-24 | Mitsubishi Materials Corp | Surface coated cutting tool having hard coating layer exhibiting excellent chipping resistance |
| JP2008229766A (en) * | 2007-03-20 | 2008-10-02 | Sumitomo Metal Ind Ltd | Cutting tool |
| JP2009154235A (en) * | 2007-12-26 | 2009-07-16 | Mitsubishi Materials Corp | Surface coated cutting tool |
| CN108262482A (en) * | 2016-12-31 | 2018-07-10 | 上海精韧激光科技有限公司 | Hard material green body and its manufacturing method and purposes |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008093769A (en) * | 2006-10-10 | 2008-04-24 | Mitsubishi Materials Corp | Surface coated cutting tool having hard coating layer exhibiting excellent chipping resistance |
| JP2008229766A (en) * | 2007-03-20 | 2008-10-02 | Sumitomo Metal Ind Ltd | Cutting tool |
| JP2009154235A (en) * | 2007-12-26 | 2009-07-16 | Mitsubishi Materials Corp | Surface coated cutting tool |
| CN108262482A (en) * | 2016-12-31 | 2018-07-10 | 上海精韧激光科技有限公司 | Hard material green body and its manufacturing method and purposes |
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