JP2014166657A - Surface-coated cutting tool having hard coating layer exerting excellent wear resistance in high-speed cutting - Google Patents
Surface-coated cutting tool having hard coating layer exerting excellent wear resistance in high-speed cutting Download PDFInfo
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Abstract
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この発明は、高熱発生を伴うステンレス鋼等の高速ミーリング加工において、硬質被覆層が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。 The present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool) that exhibits excellent wear resistance in a hard coating layer in high-speed milling processing of stainless steel or the like with high heat generation.
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）下部層が、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）上部層が、化学蒸着形成された、１〜１５μｍの平均層厚を有する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工具が知られており、この被覆工具が、例えば各種の鋼や鋳鉄などの切削加工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) 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 of the lower layers. A Ti compound layer consisting of two 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) an α-type aluminum oxide (hereinafter referred to as Al 2 O 3 ) layer having an average layer thickness of 1 to 15 μm, in which the upper layer is formed by chemical vapor deposition;
A coated tool formed by forming a hard coating layer composed of the above (a) and (b) is known, and this coated tool is also used for cutting various steels and cast irons, for example. Are known.
例えば、特許文献１に示すように、工具基体表面に、Ｔｉ化合物層とＡｌ２Ｏ３層を被覆形成した被覆工具において、＜００１＞成長方向の柱状のαＡｌ２Ｏ３粒を含むと共に、Ａｌ２Ｏ３層の組織係数ＴＣについて、ＴＣ（００６）を１．４より大きくし、さらに、最も好ましくは４．０より大きくすることにより、硬質被覆層の密着性、硬さ、靭性を改善することが提案されている。 For example, as shown in Patent Document 1, in a coated tool in which a Ti compound layer and an Al 2 O 3 layer are coated on the surface of a tool base, the column includes α001 Al 2 O 3 grains in the <001> growth direction and Al Regarding the texture coefficient TC of the 2 O 3 layer, by making TC (006) larger than 1.4, and most preferably larger than 4.0, the adhesion, hardness, and toughness of the hard coating layer are improved. It has been proposed.
また、例えば、特許文献２に示すように、工具基体表面に、Ｔｉ化合物層とＡｌ２Ｏ３層を被覆形成した被覆工具において、Ａｌ２Ｏ３層の配向性指数ＴＣについて、ＴＣ（００６）を２より大きくし、さらに、二番目に大きい配向性指数ＴＣ（１０４）を、２＞ＴＣ（１０４）＞０．５とした被覆工具が提案されている。 For example, as shown in Patent Document 2, in a coated tool in which a Ti compound layer and an Al 2 O 3 layer are formed on the surface of a tool base, the orientation index TC of the Al 2 O 3 layer is expressed as TC (006). Has been proposed, in which the second orientation index TC (104) is 2> TC (104)> 0.5.
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するとともに、切削時の工具への熱的・機械的負荷も益々増加する傾向にある。
上記の従来被覆工具においては、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、例えば、これを、ステンレス鋼の高速ミーリング切削加工に用いた場合には、高温時にＡｌ２Ｏ３結晶粒の塑性変形（粒界すべり）が発生し、そのため耐摩耗性が不十分となり、工具寿命が短命であるという問題点があった。
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 work.Accordingly, cutting speed has been further increased, and cutting tools have been improved. Thermal and mechanical loads are also increasing.
In the above conventional coated tool, there is no problem when it is used for continuous cutting or intermittent cutting under normal conditions such as steel or cast iron. For example, this is used for high-speed milling cutting of stainless steel. In such a case, plastic deformation (grain boundary sliding) of Al 2 O 3 crystal grains occurs at a high temperature, resulting in insufficient wear resistance and a short tool life.
そこで、本発明者等は、上述のような観点から、上記の被覆工具の硬質被覆層の耐摩耗性の改善をはかるべく、硬質被覆層の上部層であるＡｌ２Ｏ３層の層構造について鋭意研究を行った結果、高負荷で高熱発生を伴うステンレス鋼の高速ミーリング切削加工において、チッピング、欠損等の発生の恐れがなく、しかも、長期の使用に亘ってすぐれた耐摩耗性を発揮する硬質被覆層の層構造についての知見を得たのである。 In view of the above, the inventors of the present invention have studied the layer structure of the Al 2 O 3 layer, which is the upper layer of the hard coating layer, in order to improve the wear resistance of the hard coating layer of the above coated tool. As a result of earnest research, there is no risk of chipping, chipping, etc. in high-speed milling of stainless steel with high load and high heat generation, and excellent wear resistance over a long period of use. The knowledge about the layer structure of the hard coating layer was obtained.
つまり、前記特許文献１、２で組織係数あるいは配向性指数と呼ばれているＴＣ値（本発明では、ＴＣ値を、以下、「配向性指数」と呼ぶ。）について検討したところ、ＴＣ（１１０）の値が２．０以上で、かつ、ＴＣ（００６）の値が１．５以上となるようなＡｌ２Ｏ３層を上部層として形成することによって、チッピング、欠損等の発生の恐れがなく、しかも、長期の使用に亘ってすぐれた耐摩耗性を発揮する硬質被覆層を備えた被覆工具を提供し得ることを見出したのである。 That is, when the TC value called the texture coefficient or the orientation index in Patent Documents 1 and 2 (in the present invention, the TC value is hereinafter referred to as “orientation index”) is examined, TC (110 value of) at least 2.0, and, by forming the Al 2 O 3 layer as the value of TC (006) is 1.5 or more as an upper layer, chipping, the risk of occurrence of defects such as In addition, the present inventors have found that a coated tool having a hard coating layer exhibiting excellent wear resistance over a long period of use can be provided.
硬質被覆層の上部層を構成する従来の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％、ＣＯ２：３〜７％、ＨＣｌ：０．３〜３％、Ｈ２Ｓ：０．０２〜０．４％、Ｈ２：残り、
反応雰囲気温度：９５０〜１１００℃、
反応雰囲気圧力：６〜１３ｋＰａ、
の条件（以下、通常条件という）で形成されている。
The conventional Al 2 O 3 layer constituting the upper layer of the hard coating layer is, for example, a normal chemical vapor deposition apparatus,
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 3~7%, HCl: 0.3~3%, H 2 S: 0.02~0.4%, H 2: remainder ,
Reaction atmosphere temperature: 950-1100 ° C.
Reaction atmosphere pressure: 6-13 kPa,
(Hereinafter referred to as normal conditions).
しかし、本発明者らは、この蒸着条件を変更し、
まず、第１段階として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％、ＣＯ２：０．５〜２％、ＨＣｌ：０．３〜３％、Ｈ２Ｓ：０．０２〜０．４％、Ｈ２：残り、
反応雰囲気温度：７５０〜９００℃、
反応雰囲気圧力：２０〜３０ｋＰａ、
の条件（通常条件に比して、ＣＯ２ガス含有割合が相対的に低く、反応雰囲気圧を相対的に高くした条件）で、Ａｌ２Ｏ３層の目標層厚の２５〜５０％の層厚になるまで蒸着を行い、
その後、第２段階として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％、ＣＯ２：３〜７％、ＨＣｌ：０．３〜３％、Ｈ２Ｓ：０．５〜１％、Ｈ２：残り、
反応雰囲気温度：９５０〜１１００℃、
反応雰囲気圧力：６〜１３ｋＰａ、
の条件（通常条件に比して、Ｈ2Ｓガスの含有割合が相対的に高い条件）で、目標層厚になるまで蒸着形成することによって、ＴＣ（１１０）の値が２．０以上で、かつ、ＴＣ（００６）の値が１．５以上となるようなＡｌ２Ｏ３層を上部層として蒸着形成することができること、そして、このような第１段階及び第２段階の条件で順次形成された柱状組織のＡｌ２Ｏ３層（以下、このＡｌ２Ｏ３層を「改質Ａｌ２Ｏ３層」という）は、粒界すべりに起因する耐塑性変形性に優れるため、偏摩耗等の発生もなくすぐれた耐摩耗性を発揮することを見出したのである。
However, the inventors changed this deposition condition,
First, as the first stage,
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 0.5~2%, HCl: 0.3~3%, H 2 S: 0.02~0.4%, H 2 :remaining,
Reaction atmosphere temperature: 750 to 900 ° C.
Reaction atmosphere pressure: 20-30 kPa,
25% to 50% of the target layer thickness of the Al 2 O 3 layer under the following conditions (conditions in which the CO 2 gas content ratio is relatively low and the reaction atmosphere pressure is relatively high compared to the normal conditions) Vapor deposition until thick,
Then, as the second stage,
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 3~7%, HCl: 0.3~3%, H 2 S: 0.5~1%, H 2: remainder,
Reaction atmosphere temperature: 950-1100 ° C.
Reaction atmosphere pressure: 6-13 kPa,
Under the above conditions (conditions in which the content ratio of the H 2 S gas is relatively high compared to the normal conditions), the value of TC (110) is 2.0 or more by vapor deposition until the target layer thickness is reached. In addition, an Al 2 O 3 layer having a value of TC (006) of 1.5 or more can be deposited as an upper layer, and sequentially under the conditions of the first stage and the second stage. the Al 2 O 3 layer of the formed columnar structure (hereinafter, the the Al 2 O 3 layer as "reforming the Al 2 O 3 layer") is excellent in plastic deformation resistance due to the grain boundary sliding, uneven wear It has been found that it exhibits excellent wear resistance without the occurrence of or the like.
本発明の被覆工具は、Ｔｉ化合物層からなる下部層と、前記改質Ａｌ２Ｏ３層からなる上部層を備えることにより、ステンレス鋼の高速切削において、チッピング、欠損等の発生の恐れがなく、しかも、長期の使用に亘ってすぐれた耐摩耗性を発揮することができるのである。 The coated tool of the present invention includes a lower layer made of a Ti compound layer and an upper layer made of the modified Al 2 O 3 layer, so that there is no risk of chipping, chipping, etc. in high-speed cutting of stainless steel. In addition, excellent wear resistance can be exhibited over a long period of use.
この発明は、上記の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で構成された工具基体の表面に、
（ａ）下部層として、１〜７μｍの合計平均層厚を有する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層以上からなるＴｉ化合物層、
（ｂ）上部層として、（１１０）面の配向性指数ＴＣ（１１０）の値が２.０以上、かつ、（００６）面の配向性指数ＴＣ（００６）の値が１．５以上である０．５〜５μｍの平均層厚を有する柱状組織のＡｌ２Ｏ３層、
以上（ａ）および（ｂ）からなる硬質被覆層が、１．５〜１０μｍの全体平均層厚で被覆形成された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,
`` On the surface of the tool base made of tungsten carbide base cemented carbide,
(A) As a lower layer, one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer, and carbonitride oxide layer having a total average layer thickness of 1 to 7 μm A Ti compound layer comprising:
(B) As an upper layer, the value of the orientation index TC (110) of the (110) plane is 2.0 or more, and the value of the orientation index TC (006) of the (006) plane is 1.5 or more. A columnar textured Al 2 O 3 layer having an average layer thickness of 0.5-5 μm,
A surface-coated cutting tool, wherein the hard coating layer comprising the above (a) and (b) is coated with an overall average layer thickness of 1.5 to 10 μm. "
It has the characteristics.
つぎに、この発明の被覆工具の硬質被覆層の構成層について、詳細に説明する。
下部層：
ＴｉＣ層、ＴｉＮ層、ＴｉＣＮ層（ｌ−ＴｉＣＮを含む）ＴｉＣＯ層、ＴｉＣＮＯ層のうちの１層または２層以上からなるＴｉ化合物層は、自体が高温強度を有し、これの存在によって硬質被覆層が高温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性向上に寄与する作用をもつが、その合計平均層厚が１μｍ未満では、長期の使用に亘って十分な耐摩耗性を発揮することができず、一方その合計平均層厚が７μｍを越えると、ステンレス鋼の高速切削加工でチッピングを起し易くなることから、その合計平均層厚を１〜７μｍと定めた。
Next, the constituent layers of the hard coating layer of the coated tool of the present invention will be described in detail.
Lower layer:
Ti compound layer consisting of one or more of TiC layer, TiN layer, TiCN layer (including 1-TiCN) TiCO layer, TiCNO layer itself has high temperature strength and hard coating due to its presence In addition to having high-temperature strength, the layer adheres firmly to both the tool base and the upper Al 2 O 3 layer, and thus has an effect of contributing to improved adhesion of the hard coating layer to the tool base. However, if the total average layer thickness is less than 1 μm, sufficient wear resistance cannot be exhibited over a long period of use, while if the total average layer thickness exceeds 7 μm, high-speed cutting of stainless steel Since it becomes easy to cause chipping, the total average layer thickness was determined to be 1 to 7 μm.
上部層（改質Ａｌ２Ｏ３層）：
改質Ａｌ２Ｏ３層からなる上部層は、すぐれた高温硬さと耐熱性を有し、さらに、粒界すべりに起因する塑性変形性にすぐれることによって、偏摩耗の発生もなく、硬質被覆層の耐摩耗性向上に寄与する。
改質Ａｌ２Ｏ３層は、既に述べたように、例えば、以下の方法によって成膜することができる。
例えば、通常の化学蒸着装置にて、
まず、≪第１段階≫として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％、ＣＯ２：０．５〜２％、ＨＣｌ：０．３〜３％、Ｈ２Ｓ：０．０２〜０．４％、Ｈ２：残り、
反応雰囲気温度：７５０〜９００℃、
反応雰囲気圧力：２０〜３０ｋＰａ、
の条件（通常条件に比して、ＣＯ２ガス含有割合が相対的に低く、反応雰囲気圧を相対的に高くした条件）で、Ａｌ２Ｏ３層の目標層厚の２５〜５０％の層厚になるまで蒸着を行い、
その後、≪第２段階≫として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％、ＣＯ２：３〜７％、ＨＣｌ：０．３〜３％、Ｈ２Ｓ：０．５〜１％、Ｈ２：残り、
反応雰囲気温度：９５０〜１１００℃、
反応雰囲気圧力：６〜１３ｋＰａ、
の条件（通常条件に比して、Ｈ2Ｓガスの含有割合が相対的に高い条件）で、目標層厚になるまで蒸着形成することによって、ＴＣ（１１０）の値が２．０以上で、かつ、ＴＣ（００６）の値が１．５以上となるような改質Ａｌ２Ｏ３層を上部層として蒸着形成することができる。
この改質Ａｌ２Ｏ３層は、すぐれた高温硬さと耐熱性を示すばかりでなく、粒界すべりに起因する耐塑性変形性に優れるため、高負荷で高熱発生を伴うステンレス鋼の高速ミーリング切削加工でも、偏摩耗等の発生もなくすぐれた耐摩耗性を発揮する。
Upper layer (modified Al 2 O 3 layer):
The upper layer composed of the modified Al 2 O 3 layer has excellent high-temperature hardness and heat resistance, and further has excellent plastic deformation due to grain boundary sliding, so that there is no occurrence of uneven wear and a hard coating. Contributes to improved wear resistance of the layer.
As described above, the modified Al 2 O 3 layer can be formed by the following method, for example.
For example, in a normal chemical vapor deposition system,
First, as «First Stage»
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 0.5~2%, HCl: 0.3~3%, H 2 S: 0.02~0.4%, H 2 :remaining,
Reaction atmosphere temperature: 750 to 900 ° C.
Reaction atmosphere pressure: 20-30 kPa,
25% to 50% of the target layer thickness of the Al 2 O 3 layer under the following conditions (conditions in which the CO 2 gas content ratio is relatively low and the reaction atmosphere pressure is relatively high compared to the normal conditions) Vapor deposition until thick,
Then, as «second stage»
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 3~7%, HCl: 0.3~3%, H 2 S: 0.5~1%, H 2: remainder,
Reaction atmosphere temperature: 950-1100 ° C.
Reaction atmosphere pressure: 6-13 kPa,
Under the above conditions (conditions in which the content ratio of the H 2 S gas is relatively high compared to the normal conditions), the value of TC (110) is 2.0 or more by vapor deposition until the target layer thickness is reached. In addition, a modified Al 2 O 3 layer having a TC (006) value of 1.5 or more can be deposited as an upper layer.
This modified Al 2 O 3 layer not only exhibits excellent high-temperature hardness and heat resistance, but also has excellent plastic deformation resistance due to grain boundary sliding, so high-speed milling of stainless steel with high load and high heat generation Even in processing, it exhibits excellent wear resistance without the occurrence of uneven wear.
また、上記改質Ａｌ２Ｏ３層について、Ｘ線回折により、（０１２）面、（１０４）面、（１１０）面、（００６）面、（１１３）面、（２０２）面、（０２４）面及び（１１６）面の反射強度を求め、これらの値から、（１１０）面の配向性指数ＴＣ（１１０）および（００６）面の配向性指数ＴＣ（００６）の値を求めたところ、改質Ａｌ２Ｏ３層ではＴＣ（１１０）の値が２．０以上で、かつ、ＴＣ（００６）の値は１．５以上であった。
なお、従来Ａｌ２Ｏ３層では、ＴＣ（１１０）およびＴＣ（００６）の値は、それぞれ、
０．１〜０．８、２.８〜５.７であった（表７参照）。
なお、本発明でいう（１１０）面の配向性指数ＴＣ（１１０）および（００６）面の配向性指数ＴＣ（００６）は、上部層を構成するＡｌ２Ｏ３層についてＸ線回折を行った際の（ｈｋｌ）面から得られるＸ線回折のピーク強度値をＩ（ｈｋｌ）、ＪＣＰＤＳカードＮｏ．４６−１２１２記載の（ｈｋｌ）面の標準回折強度をＩ０（ｈｋｌ）とした場合、
であるとして定義される。ここで、（ｈｋｌ）は（０１２）、（１０４）、（１１０）、（００６）、（１１３）、（２０２）、（０２４）、（１１６）の８面である。
Further, the modified Al 2 O 3 layer was subjected to (012) plane, (104) plane, (110) plane, (006) plane, (113) plane, (202) plane, (024) by X-ray diffraction. The reflection intensity of the plane and the (116) plane was obtained, and from these values, the values of the orientation index TC (110) of the (110) plane and the orientation index TC (006) of the (006) plane were obtained. In the quality Al 2 O 3 layer, the value of TC (110) was 2.0 or more, and the value of TC (006) was 1.5 or more.
In the conventional Al 2 O 3 layer, the values of TC (110) and TC (006) are respectively
0.1 to 0.8 and 2.8 to 5.7 (see Table 7).
The (110) plane orientation index TC (110) and (006) plane orientation index TC (006) referred to in the present invention were obtained by performing X-ray diffraction on the Al 2 O 3 layer constituting the upper layer. The peak intensity value of X-ray diffraction obtained from the (hkl) plane is I (hkl), JCPDS card no. When the standard diffraction intensity of the (hkl) plane described in 46-1212 is I 0 (hkl),
Is defined as Here, (hkl) is the eight faces (012), (104), (110), (006), (113), (202), (024), and (116).
上記改質Ａｌ２Ｏ３層の配向性指数ＴＣ（１１０）およびＴＣ（００６）について、ＴＣ（１１０）が２未満である場合には、Ａｌ２Ｏ３結晶粒の粒界すべりを抑制するには十分でないため、偏摩耗の発生を防止することができず、そのため、長期の使用に亘って十分な耐摩耗性を発揮することができず、また、ＴＣ（００６）が１．５未満である場合には、Ａｌ２Ｏ３層の靭性が不足するため、十分な耐チッピング性、耐欠損性を発揮することができない。
したがって、本発明では、上部層の改質Ａｌ２Ｏ３層の配向性指数ＴＣ（１１０）およびＴＣ（００６）を、それぞれ、２.０以上、１．５以上と定めた。
In the case of the orientation index TC (110) and TC (006) of the modified Al 2 O 3 layer, when the TC (110) is less than 2, the grain boundary slip of the Al 2 O 3 crystal grains is suppressed. Is not sufficient, it is not possible to prevent the occurrence of uneven wear, so that sufficient wear resistance cannot be exhibited over a long period of use, and TC (006) is less than 1.5. In some cases, the toughness of the Al 2 O 3 layer is insufficient, so that sufficient chipping resistance and fracture resistance cannot be exhibited.
Therefore, in the present invention, the orientation indexes TC (110) and TC (006) of the modified Al 2 O 3 layer of the upper layer are set to 2.0 or more and 1.5 or more, respectively.
上部層である改質Ａｌ２Ｏ３層の層厚は、０．５μｍ未満では長期の使用に亘って十分な耐摩耗性を発揮することはできず、一方、５μｍを超えると耐チッピング性が低下するため、改質Ａｌ２Ｏ３層の層厚は０．５〜５μｍと定めた。
また、下部層と上部層からなる硬質被覆層の全体平均層厚は、１．５μｍ未満では長期の使用に亘っての十分な耐摩耗性を発揮し得ず、一方、全体平均層厚が１０μｍを超えると、チッピング、欠損が発生し易くなることから、硬質被覆層の全体平均層厚は、１．５〜１０μｍと定めた。
If the thickness of the modified Al 2 O 3 layer, which is the upper layer, is less than 0.5 μm, sufficient wear resistance cannot be exhibited over a long period of use, while if it exceeds 5 μm, chipping resistance is not achieved. In order to decrease, the layer thickness of the modified Al 2 O 3 layer was determined to be 0.5 to 5 μm.
Further, if the overall average layer thickness of the hard coating layer composed of the lower layer and the upper layer is less than 1.5 μm, sufficient wear resistance over a long period of use cannot be exhibited, while the overall average layer thickness is 10 μm. If it exceeds 1, chipping and defects are likely to occur. Therefore, the overall average layer thickness of the hard coating layer was determined to be 1.5 to 10 μm.
また、本発明は、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。
さらに、本発明は、改質Ａｌ２Ｏ３層の表面に、表面の平滑化等の目的で、機械的処理（例えば、ウエットブラスト処理、ブラシ処理、弾性砥石処理）等を施すことを何ら制限するものではない。
Further, in the present invention, 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 is 0.1 to 1 μm may be sufficient, and 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 for an average layer thickness of up to 1 μm.
Furthermore, the present invention is not limited to subjecting the surface of the modified Al 2 O 3 layer to mechanical treatment (for example, wet blast treatment, brush treatment, elastic grindstone treatment) or the like for the purpose of smoothing the surface. Not what you want.
この発明の被覆工具は、高負荷で高熱発生を伴うステンレス鋼の高速ミーリング切削加工に供した場合でも、硬質被覆層の上部層の改質Ａｌ２Ｏ３層が、すぐれた硬度と耐熱性に加え、すぐれた耐塑性変形性を示すことから、チッピング、欠損、偏摩耗等の発生もなく、長期の使用に亘って、すぐれた耐摩耗性を発揮するものである。 Even when the coated tool of the present invention is subjected to high-speed milling of stainless steel with high load and high heat generation, the modified Al 2 O 3 layer of the upper layer of the hard coating layer has excellent hardness and heat resistance. In addition, since excellent plastic deformation resistance is exhibited, there is no occurrence of chipping, chipping, uneven wear, etc., and excellent wear resistance is exhibited over a long period of use.
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２〜５μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ3Ｃ2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、表面を研磨し、切刃部にホーニング加工を施すことによりＩＳＯ・ＳＥＥＮ１２０３に規定するインサート形状をもったＷＣ基超硬合金製の工具基体Ａ〜Ｃをそれぞれ製造した。 As raw material powders, WC powder, TiC powder, ZrC powder, TaC powder, NbC powder, Cr 3 C 2 powder, and Co powder each having an average particle diameter of 2 to 5 μm were prepared. Then, after adding wax, ball mill mixing in acetone for 24 hours, drying under reduced pressure, press-molding into a green compact of a predetermined shape at a pressure of 98 MPa. Specified in ISO / SEEN1203 by vacuum sintering in vacuum at a predetermined temperature in the range of 1370 to 1470 ° C. for 1 hour, after sintering, polishing the surface, and honing the cutting edge WC base cemented carbide tool bases A to C each having an insert shape were manufactured.
（ａ） つぎに、これらの工具基体Ａ〜Ｃの表面に、通常の化学蒸着装置を用い、硬質被覆層の下部層として、Ｔｉ化合物層を表２に示される条件で、表５に示される組み合わせで、かつ同じく表５に示される目標層厚で蒸着形成し、
（ｂ）ついで、改質Ａｌ２Ｏ３層を、表３に示す条件、即ち、
まず、第１段階として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％の範囲内の所定量、ＣＯ２：０．５〜２％の範囲内の所定量、ＨＣｌ：０．３〜３％の範囲内の所定量、Ｈ２Ｓ：０．０２〜０．４％の範囲内の所定量、Ｈ２：残り、
反応雰囲気温度：７５０〜９００℃の範囲内の所定温度、
反応雰囲気圧力：２０〜３０ｋＰａの範囲内の所定圧力、
の条件で、目標層厚の約２５〜５０％の層厚となるまで蒸着し、
その後、第２段階として、
反応ガス組成：容量％で、ＡｌＣｌ３：１〜５％の範囲内の所定量、ＣＯ２：３〜７％の範囲内の所定量、ＨＣｌ：０．３〜３％の範囲内の所定量、Ｈ２Ｓ：０．５〜１％の範囲内の所定量、Ｈ２：残り、
反応雰囲気温度：９５０〜１１００℃の範囲内の所定温度、
反応雰囲気圧力：６〜１３ｋＰａの範囲内の所定圧力、
の条件で、表６に示される目標層厚になるまで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。
(A) Next, the surface of these tool bases A to C is shown in Table 5 under the conditions shown in Table 2 under the conditions shown in Table 2 as a lower layer of the hard coating layer using a normal chemical vapor deposition apparatus. In combination and vapor deposition with the target layer thickness also shown in Table 5,
(B) Next, the modified Al 2 O 3 layer was subjected to the conditions shown in Table 3, that is,
First, as the first stage,
By volume%, AlCl 3:: Reaction gas composition predetermined amount within a range of 1~5%, CO 2: the predetermined amount in the range 0.5% to 2% of, HCl: in the 0.3 to 3% range Predetermined amount, H 2 S: predetermined amount within the range of 0.02 to 0.4%, H 2 : remaining,
Reaction atmosphere temperature: a predetermined temperature within a range of 750 to 900 ° C,
Reaction atmosphere pressure: a predetermined pressure in the range of 20-30 kPa,
Under the conditions, vapor deposition until reaching a layer thickness of about 25-50% of the target layer thickness,
Then, as the second stage,
Reaction gas composition:% by volume, AlCl 3 : a predetermined amount in a range of 1 to 5%, CO 2 : a predetermined amount in a range of 3 to 7%, HCl: a predetermined amount in a range of 0.3 to 3% , H 2 S: a predetermined amount within the range of 0.5 to 1%, H 2 : remaining,
Reaction atmosphere temperature: a predetermined temperature within a range of 950 to 1100 ° C.,
Reaction atmosphere pressure: a predetermined pressure within a range of 6 to 13 kPa,
Under this condition, the present coated tools 1 to 10 were produced by vapor deposition until the target layer thickness shown in Table 6 was reached.
また、比較の目的で、硬質被覆層の下部層として、Ｔｉ化合物層を表２に示される条件で、表５に示される組み合わせで、かつ同じく表５に示される目標層厚で蒸着形成し、さらに上部層としてのＡｌ２Ｏ３層を、表４に示される条件で、かつ表７に示される目標層厚で蒸着形成することにより、従来被覆工具１〜１０をそれぞれ製造した。 For the purpose of comparison, as a lower layer of the hard coating layer, a Ti compound layer is formed by vapor deposition in the combination shown in Table 5 and with the target layer thickness shown in Table 5 under the conditions shown in Table 2. Further, Al 2 O 3 layers as upper layers were formed by vapor deposition under the conditions shown in Table 4 and with the target layer thicknesses shown in Table 7, thereby producing the conventional coated tools 1 to 10, respectively.
上記本発明被覆工具および従来被覆工具のＡｌ２Ｏ３層についてＸ線回折を行い、（０１２）,（１０４）,（１１０）,（００６）,（１１３）,（２０２）,（０２４）,（１１６）の各面からのＸ線回折強度を測定することにより、ＴＣ（１１０）、ＴＣ（００６）をそれぞれ求めた。
表６、７にこれらの値を示す。
X-ray diffraction was performed on the Al 2 O 3 layer of the present invention coated tool and the conventional coated tool, and (012), (104), (110), (006), (113), (202), (024), TC (110) and TC (006) were obtained by measuring the X-ray diffraction intensity from each surface of (116).
Tables 6 and 7 show these values.
さらに、上記の本発明被覆工具１〜１０および従来被覆工具１〜１０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。 Furthermore, when the thickness of the constituent layer of the hard coating layer of the present invention coated tools 1 to 10 and the conventional coated tools 1 to 10 was measured using the scanning electron microscope (same longitudinal section measurement), both targets The average layer thickness (average value of 5-point measurement) substantially the same as the layer thickness was shown.
つぎに、上記本発明被覆工具１〜１０及び従来被覆工具１〜１０について、以下に示す条件で、乾式高速ミーリング切削加工試験を実施し、加工パス数をカウントした。（加工する面を1回切削することを１パスとしている）
加工パス数のカウントは、切れ刃逃げ面の摩耗量が基準摩耗量である０．３ｍｍに達した時点における加工パス数を基本とするが、加工の途中で切れ刃の欠損が生じた場合には、その時点で終了している加工パス数をカウントすることとする。なお、加工途中については、加工パス数としてカウントしない。
Next, a dry high-speed milling cutting test was performed on the above-described inventive coated tools 1 to 10 and conventional coated tools 1 to 10 under the following conditions, and the number of machining passes was counted. (Cut once the surface to be processed is one pass)
Counting the number of machining passes is based on the number of machining passes when the amount of wear on the cutting edge flank reaches the standard wear amount of 0.3 mm, but when the cutting edge is broken during machining. Is to count the number of machining passes completed at that time. Note that the number of machining passes is not counted during machining.
被削材：ＪＩＳ・ＳＵＳ３０４のブロック材（幅５０ｍｍ 長さ２００ｍｍ）
切削速度：３５０ｍ／ｍｉｎ、
切り込み：ａｅ ５０ｍｍ、ａｐ １．５ｍｍ、
一刃送り量：０．２ｍｍ／刃、
（通常の切削速度は、２００ｍ/ｍｉｎ）、
表８に、上記切削試験の結果を示す。
Work material: Block material of JIS / SUS304 (width 50mm length 200mm)
Cutting speed: 350 m / min,
Incision: ae 50 mm, ap 1.5 mm,
Single-blade feed rate: 0.2 mm / tooth,
(Normal cutting speed is 200 m / min),
Table 8 shows the results of the cutting test.
表６〜８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が、ＴＣ（１１０）の値が２.０以上、かつ、ＴＣ（００６）の値が１．５以上である柱状組織の改質Ａｌ２Ｏ３層で構成されていることから、高熱発生を伴うステンレス鋼の高速ミーリング切削加工でも、前記改質Ａｌ２Ｏ３層が、粒界すべりの発生に起因する塑性変形による偏摩耗の発生を抑制するとともに、すぐれた耐チッピング性、耐欠損性を発揮することにより、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、ＴＣ（１１０）の値が０.１〜０.８、あるいは、ＴＣ（００６）の値が２．８〜５．７である硬質被覆層の上部層が従来Ａｌ２Ｏ３層である従来被覆工具１〜１０においては、特に、上部層のチッピング、欠損、偏摩耗発生によって、耐摩耗性が劣り、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 6 to 8, in the coated tools 1 to 10 of the present invention, the upper layer of the hard coating layer has a TC (110) value of 2.0 or more and a TC (006) value of 1. since it is 5 or more in which consists in modifying the Al 2 O 3 layer of columnar structure, also of stainless high-speed milling machining of steels with high heat generation, the reforming the Al 2 O 3 layer is the occurrence of grain boundary sliding In addition to suppressing the occurrence of uneven wear due to plastic deformation caused by the above, it exhibits excellent wear resistance over a long period of use by exhibiting excellent chipping resistance and fracture resistance.
On the other hand, the upper layer of the hard coating layer having a TC (110) value of 0.1 to 0.8 or a TC (006) value of 2.8 to 5.7 is conventionally Al 2 O 3. In the conventional coated tools 1 to 10 which are layers, it is apparent that the wear resistance is inferior due to chipping, chipping and partial wear of the upper layer, and the service life is reached in a relatively short time.
上述のように、この発明の被覆工具は、ステンレス鋼の高速ミーリング切削加工においてすぐれた特性を示し、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 exhibits excellent characteristics in high-speed milling cutting of stainless steel and exhibits excellent cutting performance over a long period of time. It can cope with labor saving, energy saving and cost reduction of processing sufficiently satisfactorily.
Claims (1)
（ａ）下部層として、１〜７μｍの合計平均層厚を有する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層以上からなるＴｉ化合物層、
（ｂ）上部層として、（１１０）面の配向性指数ＴＣ（１１０）の値が２.０以上、かつ、（００６）面の配向性指数ＴＣ（００６）の値が１．５以上である０．５〜５μｍの平均層厚を有する柱状組織のＡｌ２Ｏ３層、
以上（ａ）および（ｂ）からなる硬質被覆層が、１．５〜１０μｍの全体平均層厚で被覆形成されたことを特徴とする表面被覆切削工具。
On the surface of the tool base made of tungsten carbide base cemented carbide,
(A) As a lower layer, one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer, and carbonitride oxide layer having a total average layer thickness of 1 to 7 μm A Ti compound layer comprising:
(B) As an upper layer, the value of the orientation index TC (110) of the (110) plane is 2.0 or more, and the value of the orientation index TC (006) of the (006) plane is 1.5 or more. A columnar textured Al 2 O 3 layer having an average layer thickness of 0.5-5 μm,
A surface-coated cutting tool, wherein the hard coating layer comprising the above (a) and (b) is coated with an overall average layer thickness of 1.5 to 10 μm.
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| WO2017115987A1 (en) * | 2015-12-29 | 2017-07-06 | 한국야금 주식회사 | Hard coating for cutting tool |
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| WO2021250841A1 (en) * | 2020-06-11 | 2021-12-16 | 住友電工ハードメタル株式会社 | Cutting tool |
| WO2021250840A1 (en) * | 2020-06-11 | 2021-12-16 | 住友電工ハードメタル株式会社 | Cutting tool |
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| JPH10156606A (en) * | 1996-11-29 | 1998-06-16 | Hitachi Metals Ltd | Aluminum oxide coating tool and manufacture thereof |
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