JP5234354B2 - Surface coated cutting tool with excellent heat plastic deformation and interlayer adhesion strength - Google Patents
Surface coated cutting tool with excellent heat plastic deformation and interlayer adhesion strength Download PDFInfo
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この発明は、硬質被覆層がすぐれた熱遮蔽効果を有するとともにすぐれた層間密着強度を有することから、高熱発生を伴う鋼等の高速切削加工においても、熱塑性変形、チッピングを発生することなく、長期の使用に亘ってすぐれた耐摩耗性を発揮する表面被覆切削工具（以下、被覆工具という）に関するものである。 In the present invention, since the hard coating layer has an excellent heat shielding effect and an excellent interlayer adhesion strength, even in high-speed cutting such as steel accompanied by high heat generation, it does not generate thermoplastic deformation and chipping for a long time. The present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool) that exhibits excellent wear resistance over the use of the above.
特許文献１に示すように、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、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の全体平均層厚を有するＴｉ化合物層、
（ｂ）上部層として、０．０１〜１０質量％のＹ（イットリウム）を含有し、かつ、該Ｙ（イットリウム）がＡｌ2Ｏ3の粒界に存在してなるＹ含有Ａｌ2Ｏ3層、
上記（ａ）、（ｂ）からなる硬質被覆層を蒸着形成してなる被覆工具（以下、従来被覆工具という）が知られており、この従来被覆工具はＡｌ2Ｏ3の結晶粒界強度が高められているため、結晶粒の脱落がなく、切削耐久特性が向上することが知られている。
As shown in Patent Document 1, a substrate composed of tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet (hereinafter collectively referred to as a tool substrate). On the surface)
(A) As a lower layer, a Ti compound layer composed of one or more of a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, and a TiCNO layer, and having an overall average layer thickness of 3 to 20 μm,
(B) as the upper layer, containing 0.01 to 10 wt% of Y a (yttrium), and, Y containing the Al 2 O 3 layer in which the Y (yttrium) is present in the grain boundary of Al 2 O 3 ,
A coated tool formed by vapor-depositing a hard coating layer comprising the above (a) and (b) (hereinafter referred to as a conventional coated tool) is known, and this conventional coated tool has a grain boundary strength of Al 2 O 3. It is known that since it is enhanced, the crystal grains do not fall off and the cutting durability characteristics are improved.
また、特許文献２に示すように、耐摩耗性の複合セラミックコーティングを基材に付着させる方法として、酸化アルミニウム、酸化イットリウム或いは酸化ジルコニウムから成る連続金属酸化物相内に酸化アルミニウム、酸化イットリウム或いは酸化ジルコニウムから成る不連続金属酸化物を離散した第二相として分散させ該コーティングを形成することも知られているが、このようなコーティングで切削工具の硬質被覆層を形成した場合には、連続金属酸化物を構成する結晶粒の粒界強度が十分ではないため、厳しい切削条件下では、連続金属酸化物の結晶粒の脱落等により、満足できる工具特性を備えているとはいえない。 Further, as shown in Patent Document 2, as a method of attaching a wear-resistant composite ceramic coating to a substrate, aluminum oxide, yttrium oxide or oxidation is carried out in a continuous metal oxide phase composed of aluminum oxide, yttrium oxide or zirconium oxide. It is also known that a discontinuous metal oxide composed of zirconium is dispersed as a discrete second phase to form the coating. However, when a hard coating layer of a cutting tool is formed with such a coating, a continuous metal is formed. Since the grain boundary strength of the crystal grains constituting the oxide is not sufficient, it cannot be said that satisfactory tool characteristics are provided under severe cutting conditions due to dropping of the crystal grains of the continuous metal oxide.
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、高能率化する傾向にあるが、例えば、上記従来被覆工具においては、これを低合金鋼や炭素鋼などの通常条件の切削加工に用いた場合には特に問題はないが、特にこれを、高熱発生を伴う鋼等の高速切削加工に用いた場合には、硬質被覆層の層間密着強度および耐熱遮蔽効果が満足できるものでないため、切刃部にチッピング（微少欠け）、欠損、剥離を発生しやすくなり、また、耐熱性も十分でないため熱塑性変形による偏摩耗も生じやすくなり、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 and energy saving and further cost reduction for cutting, and along with this, cutting tends to become even faster and more efficient. For example, in the above-mentioned conventional coated tool, there is no particular problem when this is used for cutting under normal conditions such as low alloy steel and carbon steel. When used for processing, the interlaminar adhesion strength and heat-shielding effect of the hard coating layer are not satisfactory, so chipping (slight chipping), chipping and peeling are likely to occur at the cutting edge, and heat resistance is also good. Since it is not sufficient, uneven wear due to thermoplastic deformation is likely to occur, and 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、高熱発生を伴う高速切削加工に用いた場合にも、長期の使用に亘ってすぐれた耐チッピング性、耐摩耗性を発揮する被覆工具を開発すべく、鋭意研究を行った結果、以下の知見を得た。 Therefore, from the above viewpoint, the present inventors have provided a coated tool that exhibits excellent chipping resistance and wear resistance over long-term use even when used for high-speed cutting with high heat generation. As a result of earnest research to develop, the following knowledge was obtained.
上記の従来被覆工具におけるＹ含有Ａｌ2Ｏ3層は、
例えば、通常の化学蒸着装置にて、
反応ガス組成：容量％で、ＡｌＣｌ3：１〜５％、ＹＣｌ3：０．００５〜０．５％、ＣＯ2：３〜８％、Ｈ2：残り、
反応雰囲気温度： １０００〜１０２０ ℃、
反応雰囲気圧力： ５〜１０ ｋＰａ、
の条件で蒸着形成することができるが、
同じく通常の化学蒸着装置を用い、
反応ガス組成：容量％で、ＡｌＣｌ3：１〜５％、ＹＣｌ3：０．１〜０．６％、ＣＯ2：４〜８％、ＨＣｌ：１〜５％、Ｈ2Ｓ：０．１〜０．５％、Ａｒ：５〜２０％、Ｈ2：残り、
反応雰囲気温度： ９８０〜１０２０ ℃、
反応雰囲気圧力： ５〜８ ｋＰａ、
の条件で、下部層であるＴｉ化合物層の表面に化学蒸着をおこなうと、Ｙ（イットリウム）を０．１〜２原子％含有する（但し、Ｙ含有量は、各元素をモルで表した場合、Ｙ／（Ａｌ＋Ｏ＋Ｙ）×１００で表される原子％である）とともに、Ｙ（イットリウム）が、Ｙ２Ｏ３としてＡｌ２Ｏ３相中に分散したＹ２Ｏ３分散Ａｌ２Ｏ３層が上部層として蒸着形成される。
さらに、Ａｌ２Ｏ３相中に均一に分散する上記Ｙ２Ｏ３について、Ｘ線回折によりその配向性を調査すると、（２２２）、（４０−２）、（００３）、（８４０）面に回折ピークが存在するが、その中で（８４０）面の回折強度が大きく、（８４０）面の回折強度Ｉ（８４０）と、第２ピークの面の回折強度Ｉsecとの回折強度の比Ｉ（８４０）／Ｉsecの値が１．５以上であることから、上記Ｙ２Ｏ３は、（８４０）面、即ち、（２１０）面に高配向性を有することがわかる。
The Y-containing Al 2 O 3 layer in the above conventional coated tool is
For example, in a normal chemical vapor deposition system,
Reaction gas composition: by volume%, AlCl 3: 1~5%, YCl 3: 0.005~0.5%, CO 2: 3~8%, H 2: remainder,
Reaction atmosphere temperature: 1000 to 1020 ° C.,
Reaction atmosphere pressure: 5 to 10 kPa,
It can be formed under the conditions of
Similarly, using a normal chemical vapor deposition system,
Reaction gas composition: by volume%, AlCl 3: 1~5%, YCl 3: 0.1~0.6%, CO 2: 4~8%, HCl: 1~5%, H 2 S: 0.1 ~0.5%, Ar: 5~20%, H 2: remainder,
Reaction atmosphere temperature: 980 to 1020 ° C.,
Reaction atmosphere pressure: 5-8 kPa,
When chemical vapor deposition is performed on the surface of the Ti compound layer, which is the lower layer, the content of Y (yttrium) is 0.1 to 2 atomic% (provided that the Y content is expressed in terms of moles of each element) Y / (Al + O + Y) × 100) and Y (yttrium) as Y 2 O 3 is dispersed in the Al 2 O 3 phase as a Y 2 O 3 dispersed Al 2 O 3 layer. Vapor deposition is formed as an upper layer.
Furthermore, when the orientation of the Y 2 O 3 that is uniformly dispersed in the Al 2 O 3 phase is investigated by X-ray diffraction, the (222), (40-2), (003), and (840) planes are observed. There is a diffraction peak, of which the (840) plane has a high diffraction intensity, and the ratio of the diffraction intensity I (840) of the (840) plane and the diffraction intensity Isec of the second peak plane I ( Since the value of (840) / Isec is 1.5 or more, it can be seen that the Y 2 O 3 has high orientation in the (840) plane, that is, the (210) plane.
そして、下部層であるＴｉ化合物層上に、上記Ｙ２Ｏ３分散Ａｌ２Ｏ３層を蒸着形成することにより硬質被覆層を構成したところ、このような構造の硬質被覆層を有する被覆工具は、高熱発生を伴う高速切削条件下においても、一段とすぐれた層間密着強度と熱遮蔽性を有することにより、すぐれた耐チッピング性および耐摩耗性を発揮することを見出した。 Then, the Ti compound layer as the lower layer, was constituting the hard coating layer by depositing forming the Y 2 O 3 dispersed the Al 2 O 3 layer, coated tool having a hard coating layer having such a structure The present inventors have found that even under high-speed cutting conditions with high heat generation, excellent chipping resistance and wear resistance are exhibited by having excellent interlayer adhesion strength and heat shielding properties.
この発明は、上記知見に基づいてなされたものであって、
「 炭化タングステン基超硬合金または炭窒化チタン基サーメットで構成された工具基体の表面に、下部層と上部層からなる硬質被覆層が蒸着形成された表面被覆切削工具において、
（ａ）下部層は、Ｔｉの炭化物、窒化物、炭窒化物、炭酸化物および炭窒酸化物のいずれか１種又は２種以上からなる３〜２０μｍの合計層厚のＴｉ化合物層、
（ｂ）上部層は、Ｙ（イットリウム）を０．１〜２原子％含有するとともに、該Ｙ（イットリウム）は、Ｙ２Ｏ３としてＡｌ２Ｏ３相中に分散しており、さらに、該上部層についてＸ線回折を行ったときにＹ２Ｏ３の（８４０）面からの回折強度Ｉ（８４０）の値が最大回折強度を示し、かつ、他のＹ２Ｏ３の結晶面で２番目に大きい回折強度Ｉsecとの比の値Ｉ（８４０）／Ｉsecが１．５以上の値を満足するＹ２Ｏ３分散Ａｌ２Ｏ３層、
からなることを特徴とする表面被覆切削工具。」
に特徴を有するものである。
This invention has been made based on the above findings,
In a surface-coated cutting tool in which a hard coating layer composed of a lower layer and an upper layer is vapor-deposited on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
(A) The lower layer is a Ti compound layer having a total layer thickness of 3 to 20 μm made of any one or more of Ti carbide, nitride, carbonitride, carbonate and carbonitride,
(B) The upper layer contains 0.1 to 2 atomic% of Y (yttrium), and the Y (yttrium) is dispersed in the Al 2 O 3 phase as Y 2 O 3 , the maximum diffraction intensity value of the diffraction intensity I (840) from (840) plane of Y 2 O 3 when subjected to X-ray diffraction for the upper layer, and 2 at the crystal face of the other Y 2 O 3 Y 2 O 3 dispersed Al 2 O 3 layer in which the value I (840) / Isec of the ratio to the second largest diffraction intensity Isec satisfies a value of 1.5 or more,
A surface-coated cutting tool comprising: "
It has the characteristics.
以下に、この発明の被覆工具の硬質被覆層の構成層について、より詳細に説明する。
（ａ）Ｔｉ化合物層（下部層）
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層以上からなるＴｉ化合物層は、基本的には上部層であるＹ２Ｏ３分散Ａｌ２Ｏ３層の下部層として存在し、自身の具備するすぐれた靭性及び耐摩耗性によって硬質被覆層の高温強度向上に寄与するほか、工具基体とＹ２Ｏ３分散Ａｌ２Ｏ３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強度向上にも寄与する作用を有するが、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、特に高熱発生を伴う高速切削条件では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。
Below, the constituent layer of the hard coating layer of the coated tool of this invention is demonstrated in detail.
(A) Ti compound layer (lower layer)
Ti carbide (hereinafter referred to as TiC) layer, nitride (hereinafter referred to as TiN) layer, carbonitride (hereinafter referred to as TiCN) layer, carbonate (hereinafter referred to as TiCO) layer and carbonitride oxide The Ti compound layer consisting of one or more of the layers (hereinafter referred to as TiCNO) is basically present as the lower layer of the Y 2 O 3 dispersed Al 2 O 3 layer, which is the upper layer. Contributes to improving the high temperature strength of the hard coating layer by its excellent toughness and wear resistance, and firmly adheres to both the tool base and the Y 2 O 3 dispersed Al 2 O 3 layer, so that the hard coating layer Although it has an action that contributes to an improvement in adhesion strength to the tool base, if the total average layer thickness is less than 3 μm, the above-mentioned action cannot be sufficiently exhibited, while if the total average layer thickness exceeds 20 μm, High speed with high heat generation Under the cutting conditions, thermoplastic deformation is likely to occur, and this causes uneven wear. Therefore, the total average layer thickness was determined to be 3 to 20 μm.
（ｂ）Ｙ２Ｏ３分散Ａｌ２Ｏ３層（上部層）
Ｙ２Ｏ３分散Ａｌ２Ｏ３層からなる上部層は、例えば、通常の化学蒸着装置を用い、
反応ガス組成：容量％で、ＡｌＣｌ3：１〜５％、ＹＣｌ3：０．１〜０．６％、ＣＯ2：４〜８％、ＨＣｌ：１〜５％、Ｈ2Ｓ：０．１〜０．５％、Ａｒ：５〜２０％、Ｈ2：残り、
反応雰囲気温度： ９８０〜１０２０ ℃、
反応雰囲気圧力： ５〜８ ｋＰａ、
の条件で、下部層であるＴｉ化合物層の表面に化学蒸着を行うことにより、形成することができる。
(B) Y 2 O 3 dispersed Al 2 O 3 layer (upper layer)
The upper layer composed of the Y 2 O 3 dispersed Al 2 O 3 layer uses, for example, a normal chemical vapor deposition apparatus,
Reaction gas composition: by volume%, AlCl 3: 1~5%, YCl 3: 0.1~0.6%, CO 2: 4~8%, HCl: 1~5%, H 2 S: 0.1 ~0.5%, Ar: 5~20%, H 2: remainder,
Reaction atmosphere temperature: 980 to 1020 ° C.,
Reaction atmosphere pressure: 5-8 kPa,
Under the conditions, it can be formed by performing chemical vapor deposition on the surface of the Ti compound layer as the lower layer.
下部層の上に化学蒸着されたＹ２Ｏ３分散Ａｌ２Ｏ３層からなる上部層は、その構成成分であるＡｌ成分が、層の高温硬さおよび耐熱性を向上させる。
また、Ｙ換算で０．１〜２原子％（Ｙ（モル）／（Ａｌ（モル）＋Ｏ（モル）＋Ｙ（モル）×１００の値）のＹ２Ｏ３が、層の主体相を構成するＡｌ２Ｏ３相中に均一に分散する組織状態を形成することにより、下部層との層間密着強度が向上するとともに、上部層の耐熱性がより一層向上し、さらに、分散相であるＹ２Ｏ３が（２１０）面に高配向していることにより、上部層の熱遮蔽効果が高まり、熱塑性変形による偏摩耗の発生を防止する。
上部層におけるＹの含有割合が０．１原子％未満では、Ａｌ２Ｏ３相中にＹ２Ｏ３が均一に分散する組織状態を形成することができず、一方、Ｙ含有割合が２原子％を超えると、上部層の主体相を構成するＡｌ２Ｏ３層の高温強度が低下するようになるため、上部層におけるＹの含有割合を０．１〜２原子％と定めた。
また、Ｙ２Ｏ３分散Ａｌ２Ｏ３層からなる上部層の層厚が２μｍ未満では、熱遮蔽効果が十分でないため、熱塑性変形、偏摩耗の発生を防止するに不十分であり、一方、層厚が１５μｍを超えると、チッピングなどの異常損層を発生しやすくなることから、上部層の層厚は２〜１５μｍとすることが望ましい。
In the upper layer composed of the Y 2 O 3 dispersed Al 2 O 3 layer chemically vapor-deposited on the lower layer, the Al component as its constituent component improves the high temperature hardness and heat resistance of the layer.
Further, Y 2 O 3 of 0.1 to 2 atomic% (Y (mol) / (Al (mol) + O (mol) + Y (mol)) × 100 value) in terms of Y constitutes the main phase of the layer. by forming the tissue state of uniformly distributed al 2 O 3 phase, as well as improved interlayer adhesion strength between the lower layer, the heat resistance of the upper layer is further improved, further, a dispersed phase Y 2 Since O 3 is highly oriented in the (210) plane, the heat shielding effect of the upper layer is enhanced and the occurrence of uneven wear due to thermoplastic deformation is prevented.
When the content ratio of Y in the upper layer is less than 0.1 atomic%, it is impossible to form a textured state in which Y 2 O 3 is uniformly dispersed in the Al 2 O 3 phase, while the Y content ratio is 2 atoms. If it exceeds 50%, the high-temperature strength of the Al 2 O 3 layer constituting the main phase of the upper layer is lowered, so the Y content in the upper layer was determined to be 0.1 to 2 atomic%.
Further, if the thickness of the upper layer composed of the Y 2 O 3 dispersed Al 2 O 3 layer is less than 2 μm, the heat shielding effect is not sufficient, so that it is insufficient to prevent the occurrence of thermoplastic deformation and uneven wear, If the layer thickness exceeds 15 μm, an abnormal loss layer such as chipping is likely to occur. Therefore, the layer thickness of the upper layer is preferably 2 to 15 μm.
上記のとおり、この発明の被覆工具は、Ｔｉ化合物層からなる下部層上に、Ｙ（イットリウム）を０．１〜２原子％含有するとともに、該Ｙ（イットリウム）は、Ｙ２Ｏ３としてＡｌ２Ｏ３相中に分散しており、さらに、該Ｙ２Ｏ３は（２１０）面に高配向性を有するＹ２Ｏ３分散Ａｌ２Ｏ３層を上部層として蒸着形成したことにより、下部層−上部層間の層間密着強度が増すとともに、上部層の耐熱性、熱遮蔽効果が向上するため、高熱発生を伴う高速切削加工において、チッピング、欠損、剥離を生じないばかりか、熱塑性変形による偏摩耗を発生することもなく、長期の使用に亘ってすぐれた耐摩耗性を発揮し、使用寿命の一層の延命化が可能となる。 As described above, the coated tool of the present invention contains 0.1 to 2 atom% of Y (yttrium) on the lower layer made of the Ti compound layer, and Y (yttrium) is Al as Y 2 O 3. The Y 2 O 3 is dispersed in the 2 O 3 phase, and the Y 2 O 3 is deposited on the (210) plane as a top layer by depositing a Y 2 O 3 dispersed Al 2 O 3 layer having a high orientation. The interlayer adhesion strength between the upper layer and the upper layer is increased, and the heat resistance and heat shielding effect of the upper layer are improved. Therefore, not only chipping, chipping and peeling are not caused in high-speed cutting processing with high heat generation, but also the deformation due to thermoplastic deformation. No wear is generated and excellent wear resistance is exhibited over a long period of use, and the service life can be further extended.
つぎに、この発明の被覆工具を実施例により具体的に説明する。 Next, the coated tool of the present invention will be specifically described with reference to examples.
原料粉末として、いずれも２〜４μｍ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、Ｃｒ3Ｃ2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１．３Ｐａ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・ＣＮＭＧ１２０４０８ＭＡ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〜Ｅ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 2 to 4 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 1.3 Pa. After sintering, the cutting edge portion had R: 0.07 mm. The tool bases A to E made of a WC-base cemented carbide having a throwaway tip shape defined in ISO · CNMG120408MA were manufactured by performing the honing process.
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、Ｍｏ2Ｃ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・ＣＮＭＧ１２０４０８ＭＡのチップ形状をもったＴｉＣＮ基サーメット製の工具基体ａ〜ｅ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 e made of TiCN base cermet having a standard / CNMG120408MA chip shape were formed.
ついで、これらの工具基体Ａ〜Ｅおよび工具基体ａ〜ｅのそれぞれを、通常の化学蒸着装置に装入し、
まず、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、表６に示される目標層厚のＴｉ化合物層を硬質被覆層の下部層として蒸着形成し、
ついで、表４に示される条件にて、表６に示される目標層厚のＹ２Ｏ３分散Ａｌ２Ｏ３層を硬質被覆層の上部層として蒸着形成することにより本発明被覆工具１〜１０をそれぞれ製造した。
Then, each of these tool bases A to E and tool bases a to e is charged into a normal chemical vapor deposition apparatus,
First, Table 3 (l-TiCN in Table 3 indicates the conditions for forming a TiCN layer having a vertically grown crystal structure described in JP-A No. 6-8010, and other than that, a normal granular crystal structure is shown. The Ti compound layer having the target layer thickness shown in Table 6 is deposited as a lower layer of the hard coating layer under the conditions shown in FIG.
Then, under the conditions shown in Table 4, the present invention coated tool by depositing form Y 2 O 3 dispersed the Al 2 O 3 layer of the target layer thicknesses shown in Table 6 as the upper layer of the hard layer 10 Were manufactured respectively.
また、比較の目的で、硬質被覆層の下部層を表３に示される条件にて形成し、上部層を表５に示される条件（特許文献１に開示されたＹ含有Ａｌ2Ｏ3層の蒸着条件に相当）にて形成することにより、表７に示される目標層厚のＴｉ化合物層とＹ含有Ａｌ2Ｏ3層からなる硬質被覆層を設けた従来被覆工具１〜１０をそれぞれ製造した。
なお、従来被覆工具１〜１０の工具基体種別、下部層種別及び下部層厚は、それぞれ、本発明被覆工具１〜１０のそれと同じである。
For comparison purposes, the lower layer of the hard coating layer is formed under the conditions shown in Table 3, and the upper layer is formed under the conditions shown in Table 5 (the Y-containing Al 2 O 3 layer disclosed in Patent Document 1). The conventional coated tools 1 to 10 provided with a hard coating layer composed of a Ti compound layer having a target layer thickness shown in Table 7 and a Y-containing Al 2 O 3 layer were produced respectively. .
The tool base type, the lower layer type, and the lower layer thickness of the conventional coated tools 1 to 10 are the same as those of the present coated tools 1 to 10, respectively.
ついで、上記の本発明被覆工具１〜１０の硬質被覆層の上部層を構成するＹ２Ｏ３分散Ａｌ２Ｏ３層、および、従来被覆工具１〜１０の硬質被覆層の上部層を構成するＹ含有Ａｌ２Ｏ３層について、Ｘ線回折により、Ｙ２Ｏ３存在の有無と配向性を、また、エネルギー分散型Ｘ線回折装置内蔵の透過型電子顕微鏡により、結晶粒内部と結晶粒界部のＹ量を分析した。
Ｘ線回折の測定条件は次のとおりである。
通常のＸ線回折装置を用い、Ｘ線管中に設置されたＣｕ陽極（ターゲット）に対して、電圧４０ｋＶ、電流３５０ｍＡの条件で金属Ｗフィラメントから発生させた熱電子を加速照射することにより、前記Ｃｕ陽極表面から０．１５４ｎｍの波長を有する特性Ｘ線であるＣｕ−Ｋα線を発生させ、前記特性Ｘ線をＹ２Ｏ３分散Ａｌ２Ｏ３層表面、Ｙ含有Ａｌ２Ｏ３層表面に照射し、該層から散乱したＸ線のうち、該層表面に対するＸ線入射角度θと等しい角度で回折したＸ線の強度をＸ線検出器にて測定することにより行った。また、このときの測定範囲は、θ＝７．５〜６５°である。
図１に、本発明被覆工具１について測定したＸ線回折チャートを示すが、このチャートから、（２２２）、（４０−２）、（００３）、（８４０）面に回折ピークが存在するが、その中で（８４０）面の回折強度Ｉ（８４０）が一番大きく、Ｉ（８４０）と第２ピークの回折強度Ｉsecとの回折強度比Ｉ（８４０）／Ｉsecの値が１．５以上であることから、Ｙ２Ｏ３分散Ａｌ２Ｏ３層のＹ２Ｏ３相は、（８４０）面、即ち、（２１０）面に高配向性を有することがわかる。
参考のために、従来被覆工具１〜１０のＡｌ２Ｏ３相の粒界に存在するＹ２Ｏ３相についても、Ｘ線回折により、面配向性を調査した。
図２に、従来被覆工具１について測定したＸ線回折チャートを示すが、このチャートでは、Ｙ２Ｏ３回折ピークが存在していなかった。
表６、７に、Ｘ線回折で測定したＹ２Ｏ３相の有する最強面指数を示す。表６、７から、本発明被覆工具の上部層のＹ２Ｏ３相は、（２１０）面への高い配向性を示すのに対して、従来被覆工具の上部層では、Ｙ２Ｏ３相が存在していないことがわかる。
また、前記エネルギー分散型Ｘ線回折装置内蔵の透過型電子顕微鏡による結晶粒内部と結晶粒界部のＹ量の分析結果から、本発明被覆工具の上部層におけるＹ２Ｏ３相の存在個所は、結晶粒界のみではないことがわかる。
Next, the Y 2 O 3 dispersed Al 2 O 3 layer constituting the upper layer of the hard coating layer of the present invention coated tools 1 to 10 and the upper layer of the hard coating layer of the conventional coated tools 1 to 10 are configured. For Y-containing Al 2 O 3 layer, the presence and orientation of Y 2 O 3 are determined by X-ray diffraction, and the inside of crystal grains and the grain boundaries are analyzed by a transmission electron microscope built in an energy dispersive X-ray diffractometer. The amount of Y in the part was analyzed.
The measurement conditions of X-ray diffraction are as follows.
By using a normal X-ray diffractometer, a Cu anode (target) installed in an X-ray tube is accelerated and irradiated with thermoelectrons generated from a metal W filament under conditions of a voltage of 40 kV and a current of 350 mA, A Cu—Kα ray, which is a characteristic X-ray having a wavelength of 0.154 nm, is generated from the Cu anode surface, and the characteristic X-ray is generated as a Y 2 O 3 dispersed Al 2 O 3 layer surface or a Y-containing Al 2 O 3 layer surface. The X-ray intensity diffracted at an angle equal to the X-ray incident angle θ on the surface of the X-rays scattered from the layer was measured by an X-ray detector. Further, the measurement range at this time is θ = 7.5 to 65 °.
FIG. 1 shows an X-ray diffraction chart measured for the coated tool 1 of the present invention. From this chart, diffraction peaks exist on the (222), (40-2), (003), and (840) planes. Among them, the diffraction intensity I (840) of the (840) plane is the largest, and the value of the diffraction intensity ratio I (840) / Isec between I (840) and the diffraction intensity Isec of the second peak is 1.5 or more. From this, it can be seen that the Y 2 O 3 phase of the Y 2 O 3 -dispersed Al 2 O 3 layer has a high orientation in the (840) plane, that is, the (210) plane.
For reference, the surface orientation of the Y 2 O 3 phase existing at the grain boundaries of the Al 2 O 3 phase of the conventional coated tools 1 to 10 was also examined by X-ray diffraction.
FIG. 2 shows an X-ray diffraction chart measured for the conventional coated tool 1, and in this chart, no Y 2 O 3 diffraction peak was present.
Tables 6 and 7 show the strongest surface index of the Y 2 O 3 phase measured by X-ray diffraction. From Tables 6 and 7, the Y 2 O 3 phase of the upper layer of the coated tool of the present invention shows high orientation to the (210) plane, whereas the Y 2 O 3 phase of the upper layer of the conventional coated tool is shown. It can be seen that does not exist.
Further, from the result of analyzing the amount of Y inside the crystal grains and the grain boundary portion by the transmission electron microscope built in the energy dispersive X-ray diffractometer, the existence location of the Y 2 O 3 phase in the upper layer of the coated tool of the present invention is It turns out that it is not only a grain boundary.
ついで、本発明被覆工具１〜１０、従来被覆工具１〜１０の硬質被覆層の各構成層の厚さを、走査型電子顕微鏡を用いて測定（縦断面測定）したが、いずれもの場合も、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。 Next, the thickness of each constituent layer of the hard coating layer of the present invention coated tools 1 to 10 and conventional coated tools 1 to 10 was measured using a scanning electron microscope (longitudinal section measurement). The average layer thickness (average value of 5-point measurement) substantially the same as the target layer thickness was shown.
つぎに、上記の本発明被覆工具１〜１０、従来被覆工具１〜１０について、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、
被削材：ＪＩＳ・Ｓ４５Ｃの丸棒、
切削速度： ４６０ ｍ／ｍｉｎ．、
切り込み： １．５ ｍｍ、
送り： ０．３ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ａという）での炭素鋼の乾式高速連続切削試験（通常の切削速度は、２５０ｍ／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： ４００ ｍ／ｍｉｎ．、
切り込み： １．５ ｍｍ、
送り： ０．２ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ｂという）でのクロムモリブデン合金鋼の湿式高速断続切削試験（通常の切削速度は、３００ｍ／ｍｉｎ．）、
被削材：ＪＩＳ・ＳＮＣＭ４３９の丸棒、
切削速度： ３５０ ｍ／ｍｉｎ．、
切り込み： １．５ ｍｍ、
送り： ０．２ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ｃという）でのニッケルクロムモリブデン合金鋼の乾式高速連続切削試験（通常の切削速度は、２５０ｍ／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８に示した。
Next, for the above-described coated tools 1 to 10 of the present invention and the conventional coated tools 1 to 10, both are screwed to the tip of the tool steel tool with a fixing jig,
Work material: JIS / S45C round bar,
Cutting speed: 460 m / min. ,
Cutting depth: 1.5 mm,
Feed: 0.3 mm / rev. ,
Cutting time: 5 minutes,
Dry high-speed continuous cutting test of carbon steel under the following conditions (referred to as cutting condition A) (normal cutting speed is 250 m / min.),
Work material: JIS · SCM440 lengthwise equidistant 4 vertical grooved round bar,
Cutting speed: 400 m / min. ,
Cutting depth: 1.5 mm,
Feed: 0.2 mm / rev. ,
Cutting time: 5 minutes,
Wet high-speed intermittent cutting test (normal cutting speed is 300 m / min.) Of chromium-molybdenum alloy steel under the following conditions (referred to as cutting condition B),
Work material: JIS / SNCM439 round bar,
Cutting speed: 350 m / min. ,
Cutting depth: 1.5 mm,
Feed: 0.2 mm / rev. ,
Cutting time: 5 minutes,
Dry high-speed continuous cutting test of nickel chromium molybdenum alloy steel under the conditions (cutting condition C) (normal cutting speed is 250 m / min.),
In each cutting test, the flank wear width of the cutting edge was measured.
The measurement results are shown in Table 8.
表８〜１０に示される結果から、本発明被覆工具１〜１０は、硬質被覆層の上部層を構成するＹ２Ｏ３分散Ａｌ２Ｏ３層が、優れた層間密着強度、耐熱性及び熱遮蔽効果を有することから、高熱発生を伴う高速切削加工において、チッピング、欠損、剥離を生じないばかりか、熱塑性変形による偏摩耗を発生することもなく、長期の使用に亘ってすぐれた耐摩耗性を発揮する。
これに対して、硬質被覆層の上部層がＹ含有Ａｌ２Ｏ３層からなる従来被覆工具１〜１５においては、チッピング、欠損、剥離の発生あるいは熱塑性変形による偏摩耗の発生によって、比較的短時間で使用寿命に至ることが明らかである。
From the results shown in Tables 8 to 10, according to the present invention coated tools 1 to 10, the Y 2 O 3 dispersed Al 2 O 3 layer constituting the upper layer of the hard coating layer has excellent interlayer adhesion strength, heat resistance and heat. Because it has a shielding effect, it does not cause chipping, chipping or peeling in high-speed cutting with high heat generation, and does not cause uneven wear due to thermoplastic deformation. To demonstrate.
On the other hand, in the conventional coated tools 1 to 15 in which the upper layer of the hard coating layer is composed of the Y-containing Al 2 O 3 layer, it is relatively short due to occurrence of chipping, chipping, peeling, or partial wear due to thermoplastic deformation. It is clear that the service life is reached in time.
上述のように、この発明の被覆工具は、各種の鋼や鋳鉄などの通常条件の切削加工は勿論のこと、高熱発生を伴う高速切削加工でも、チッピング、偏摩耗等の発生なく、すぐれた耐摩耗性を示し、長期に亘ってすぐれた切削性能を発揮するものであるから、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 tool of the present invention has excellent resistance to cutting without occurrence of chipping, uneven wear, etc., even in high-speed cutting with high heat generation, as well as cutting under various conditions such as various steels and cast iron. Since it exhibits wearability and exhibits excellent cutting performance over a long period of time, it can sufficiently satisfy the high performance of cutting equipment, labor saving and energy saving of cutting, and cost reduction. .
Claims (1)
（ａ）下部層は、Ｔｉの炭化物、窒化物、炭窒化物、炭酸化物および炭窒酸化物のいずれか１種又は２種以上からなる３〜２０μｍの合計層厚のＴｉ化合物層、
（ｂ）上部層は、Ｙ（イットリウム）を０．１〜２原子％含有するとともに、該Ｙ（イットリウム）は、Ｙ２Ｏ３としてＡｌ２Ｏ３相中に分散しており、さらに、該上部層についてＸ線回折を行ったときにＹ２Ｏ３の（８４０）面からの回折強度Ｉ（８４０）の値が最大回折強度を示し、かつ、他のＹ２Ｏ３の結晶面で２番目に大きい回折強度Ｉsecとの比の値Ｉ（８４０）／Ｉsecが１．５以上の値を満足するＹ２Ｏ３分散Ａｌ２Ｏ３層、
からなることを特徴とする表面被覆切削工具。 In a surface-coated cutting tool in which a hard coating layer composed of a lower layer and an upper layer is vapor-deposited on the surface of a tool base composed of a tungsten carbide-based cemented carbide or a titanium carbonitride-based cermet,
(A) The lower layer is a Ti compound layer having a total layer thickness of 3 to 20 μm made of any one or more of Ti carbide, nitride, carbonitride, carbonate and carbonitride,
(B) The upper layer contains 0.1 to 2 atomic% of Y (yttrium), and the Y (yttrium) is dispersed in the Al 2 O 3 phase as Y 2 O 3 , the maximum diffraction intensity value of the diffraction intensity I (840) from (840) plane of Y 2 O 3 when subjected to X-ray diffraction for the upper layer, and 2 in the crystal plane other Y 2 O 3 Y 2 O 3 dispersed Al 2 O 3 layer in which the value I (840) / Isec of the ratio to the second largest diffraction intensity Isec satisfies a value of 1.5 or more,
A surface-coated cutting tool comprising:
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| CA2149567C (en) * | 1994-05-31 | 2000-12-05 | William C. Russell | Coated cutting tool and method of making same |
| JP3910881B2 (en) * | 2002-06-03 | 2007-04-25 | 日立ツール株式会社 | Oxide coating tool |
| JP4569862B2 (en) * | 2004-03-02 | 2010-10-27 | 三菱マテリアル株式会社 | Surface coated cermet cutting tool with excellent chipping resistance with hard coating layer |
| JP5118381B2 (en) * | 2007-04-10 | 2013-01-16 | エリコン・トレーディング・アクチェンゲゼルシャフト，トリュープバッハ | Tool with protective layer system |
-
2009
- 2009-01-07 JP JP2009001305A patent/JP5234354B2/en active Active
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| JP2010158733A (en) | 2010-07-22 |
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