JP2007160459A - Surface coated cermet cutting tip having hard coating layer exhibiting superior chipping resistance in high speed cutting - Google Patents
Surface coated cermet cutting tip having hard coating layer exhibiting superior chipping resistance in high speed cutting Download PDFInfo
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この発明は、特に各種の鋼や鋳鉄などの高速切削加工に用いた場合に、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スローアウエイチップ（以下、被覆切削チップという）に関するものである。 The present invention relates to a surface-coated cermet cutting throwaway tip (hereinafter referred to as a coated cutting tip) that exhibits excellent chipping resistance with a hard coating layer, particularly when used for high-speed cutting of various types of steel and cast iron. Is.
従来、一般に、図３に概略斜視図で示される通り、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、かつ中心部に工具取りつけ孔を有する基体（以下、これらを総称してチップ基体という）の切刃稜線部を含むすくい面および逃げ面の全面に、
下部層として、炭化チタン（以下、ＴｉＣで示す）層、窒化チタン（以下、同じくＴｉＮで示す）層、炭窒化チタン（以下、ＴｉＣＮで示す）層、炭酸化チタン（以下、ＴｉＣＯで示す）層、および炭窒酸化チタン（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の全体平均層厚を有するＴｉ化合物層、
上部層として、１〜１５μｍの平均層厚を有し、かつ化学蒸着した状態で酸化アルミニウムと酸化ジルコニウムの２相混合酸化物層（以下、Ａｌ２Ｏ３−ＺｒＯ２層で示す）、
以上で構成された硬質被覆層を蒸着形成してなる被覆切削チップが知られており、この被覆切削チップが、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ることは良く知られている。
そして、上記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）は、次のような条件で化学蒸着することにより形成されることが知られている。
（イ）反応ガス組成（体積％）
ＡｌＣｌ３： １〜１０ ％、
ＺｒＣｌ４： ０．０１〜１０ ％、
ＣＯ2 ： １〜３０ ％、
ＨＣｌ： １〜３０ ％、
Ｈ２Ｓ： ０．０１〜１ ％、
Ｈ2：残り、
（ロ）反応雰囲気温度 ： ９００〜１０５０ ℃、
（ハ）反応雰囲気圧力 ： ４〜７０ ｋＰａ（３０〜５２５ ｔｏｒｒ）、
また、上記の被覆切削チップにおいて、これの硬質被覆層の構成層は、一般に粒状結晶組織を有し、さらに、下部層である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。
さらに、被覆切削チップの硬質被覆層を構成する上部層の表面を、切削性能を向上させる目的でウエットブラスト処理して、平滑化することも知られている。
As a lower layer, a titanium carbide (hereinafter referred to as TiC) layer, a titanium nitride (hereinafter also referred to as TiN) layer, a titanium carbonitride (hereinafter referred to as TiCN) layer, a titanium carbonate (hereinafter referred to as TiCO) layer And a Ti compound layer comprising one or more of titanium carbonitride oxide (hereinafter referred to as TiCNO) layers and having an overall average layer thickness of 3 to 20 μm,
As an upper layer, it has an average layer thickness of 1 to 15 μm, and is a two-phase mixed oxide layer of aluminum oxide and zirconium oxide in a state of chemical vapor deposition (hereinafter referred to as an Al 2 O 3 —ZrO 2 layer),
A coated cutting tip formed by vapor-depositing the hard coating layer constituted as described above is known, and it is well known that this coated cutting tip is used for continuous cutting and intermittent cutting of various steels and cast irons, for example. ing.
The two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) is known to be formed by chemical vapor deposition under the following conditions.
(B) Reaction gas composition (volume%)
AlCl 3 : 1 to 10%,
ZrCl 4: 0.01~10%,
CO 2: 1~30%,
HCl: 1-30%,
H 2 S: 0.01~1%,
H 2 : Remaining
(B) Reaction atmosphere temperature: 900 to 1050 ° C.
(C) Reaction atmosphere pressure: 4 to 70 kPa (30 to 525 torr),
In the above-mentioned coated cutting tip, the constituent layer of the hard coating layer generally has a granular crystal structure, and the TiCN layer constituting the Ti compound layer as the lower layer is intended to improve the strength of the layer itself. In a normal chemical vapor deposition apparatus, a gas mixture containing organic carbonitrides is used as a reaction gas, and it is formed by chemical vapor deposition at an intermediate temperature range of 700 to 950 ° C. so that it has a vertically grown crystal structure. It is also known to do.
Furthermore, it is also known to smooth the surface of the upper layer constituting the hard coating layer of the coated cutting tip by wet blasting for the purpose of improving the cutting performance.
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、切削加工は高速化の傾向にあるが、上記の従来被覆切削チップにおいては、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、特に切削速度が３５０ｍ／ｍｉｎ．を越える高速で切削加工を行なうのに用いた場合には、硬質被覆層の上部層を構成する２相混合酸化物層にチッピング（微少欠け）が発生し易く、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 has been a strong demand for labor saving and energy saving and further cost reduction for cutting work. The cutting tip has no problem when it is used for continuous cutting or intermittent cutting under normal conditions such as steel or cast iron, but the cutting speed is 350 m / min. When used for cutting at a high speed exceeding 1, the two-phase mixed oxide layer constituting the upper layer of the hard coating layer is likely to chip (small chipping), and as a result, used in a relatively short time. The current situation is that it reaches the end of its life.
そこで、本発明者等は、上述のような観点から、上記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）が硬質被覆層の上部層を構成する被覆切削チップに着目し、特にＡｌ２Ｏ３−ＺｒＯ２層の耐チッピング性向上を図るべく研究を行った結果、
（ａ）上記の従来被覆切削チップにおける硬質被覆層の上部層を構成するＡｌ２Ｏ３−ＺｒＯ２層の表面に、ウエットブラストにて、噴射研磨材として、水との合量に占める割合で１５〜６０質量％の酸化アルミニウム（以下、Ａｌ2Ｏ3で示す）微粒を配合した研磨液を噴射して、研磨すると、前記Ａｌ２Ｏ３−ＺｒＯ２層は、準拠規格ＪＩＳ・Ｂ０６０１−１９９４に基いた測定（以下の表面粗さは全てかかる準拠規格に基いた測定値を示す）で、Ｒａ：０．３〜０．６μｍの表面粗さを示すようになるが、この結果の前記Ａｌ２Ｏ３−ＺｒＯ２層の表面を、ウエットブラストにてＲａ：０．３〜０．６μｍの表面粗さに平滑化した被覆切削チップを用いても、切削速度が３５０ｍ／ｍｉｎ．を越えた高速切削加工では切刃部におけるチッピング発生を満足に抑制することはできないこと。
Therefore, the present inventors pay attention to the coated cutting tip in which the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) constitutes the upper layer of the hard coating layer from the above viewpoint, As a result of conducting research to improve the chipping resistance of the Al 2 O 3 —ZrO 2 layer,
(A) On the surface of the Al 2 O 3 —ZrO 2 layer constituting the upper layer of the hard coating layer in the above-mentioned conventional coated cutting tip, the ratio of the wet blast to the total amount of water as the spray abrasive When a polishing liquid containing 15 to 60% by mass of aluminum oxide (hereinafter referred to as Al 2 O 3 ) fine particles is sprayed and polished, the Al 2 O 3 —ZrO 2 layer is in compliance with JIS B0601-1994. (The following surface roughness is a measured value based on such standards.) Ra: 0.3 to 0.6 μm surface roughness is obtained. Even when a coated cutting tip in which the surface of the 2 O 3 —ZrO 2 layer was smoothed to a surface roughness of Ra: 0.3 to 0.6 μm by wet blasting, the cutting speed was 350 m / min. High-speed cutting that exceeds the limit cannot effectively suppress chipping at the cutting edge.
（ｂ）一方、図２に概略斜視図で示される通り、上記の従来被覆切削チップにおける硬質被覆層の上部層を構成するＡｌ２Ｏ３−ＺｒＯ２層の切刃稜線部を含むすくい面および逃げ面の全面に、通常の化学蒸着装置を用い、通常の条件、例えば表３に示される条件で、いずれも０．１〜２．５μｍの平均層厚を有する窒化チタン（以下、ＴｉＮで示す）層と炭窒化チタン（以下、ＴｉＣＮで示す）層の２層以上の交互積層を、０．４〜５μｍの全体平均層厚で蒸着形成した状態で、
上記（ａ）におけると同じくウエットブラストにて、噴射研磨材として、水との合量に占める割合で１５〜６０質量％のＡｌ2Ｏ3微粒を配合した研磨液を噴射すると、上記ＴｉＮ層とＴｉＣＮ層の２層以上の交互積層（以下、個々にＴｉＮ研磨材層およびＴｉＣＮ研磨材層と言い、これら全体をＴｉＮ／ＴｉＣＮ研磨材層で示す）は、前記Ａｌ2Ｏ3微粒によって粉砕微粒化し、ＴｉＮ微粒およびＴｉＣＮ微粒となって前記Ａｌ2Ｏ3微粒の共存下で研磨材として作用し、硬質被覆層の上部層を構成するＡｌ２Ｏ３−ＺｒＯ２層の表面を研磨することになり、この結果研磨後の前記Ａｌ２Ｏ３−ＺｒＯ２層の表面は、Ｒａ：０．２μｍ以下の表面粗さにまで平滑化されるようになり、この上部層であるＡｌ２Ｏ３−ＺｒＯ２層の表面がＲａ：０．２μｍ以下の表面粗さに平滑化した被覆切削チップを用いて、高速切削加工を行った場合、３５０ｍ／ｍｉｎ．を越える切削速度でも切刃部におけるチッピング発生が防止され、前記硬質被覆層は長期に亘ってすぐれた耐摩耗性を発揮するようになること。
(B) On the other hand, as shown in the schematic perspective view of FIG. 2, the rake face including the cutting edge ridge portion of the Al 2 O 3 —ZrO 2 layer constituting the upper layer of the hard coating layer in the conventional coated cutting tip and On the entire surface of the flank, an ordinary chemical vapor deposition apparatus is used, and titanium nitride (hereinafter referred to as TiN hereinafter) having an average layer thickness of 0.1 to 2.5 μm under normal conditions, for example, conditions shown in Table 3. ) And two or more layers of titanium carbonitride (hereinafter referred to as TiCN) layers are vapor-deposited with an overall average layer thickness of 0.4 to 5 μm,
As in the above (a), when a polishing liquid containing 15 to 60% by mass of Al 2 O 3 fine particles as a spray abrasive is mixed with water as a spray abrasive, the TiN layer and Two or more alternating layers of TiCN layers (hereinafter referred to individually as a TiN abrasive layer and a TiCN abrasive layer, and these are shown as TiN / TiCN abrasive layers) are pulverized and atomized by the Al 2 O 3 granules. The TiN fine particles and TiCN fine particles act as an abrasive in the presence of the Al 2 O 3 fine particles, and the surface of the Al 2 O 3 —ZrO 2 layer constituting the upper layer of the hard coating layer is polished. As a result, the surface of the Al 2 O 3 —ZrO 2 layer after polishing is smoothed to a surface roughness of Ra: 0.2 μm or less, and this upper layer is Al 2 O 3 —ZrO. Table of 2-layer There Ra: 0.2 [mu] m by using a coated cutting chips smoothing surface roughness of not more than, in the case of performing high-speed cutting, 350 meters / min. Chipping at the cutting edge is prevented even at a cutting speed exceeding 1, and the hard coating layer exhibits excellent wear resistance over a long period of time.
（ｃ）上記の通り、切削速度が３５０ｍ／ｍｉｎ．を越えた高速切削加工では、被覆切削チップの切刃部に懸かる負荷はきわめて高いものになるため、特にフライス切削の場合、工具本体への被覆切削チップの取り付けに際しては、きわめて高い締め付け力で取り付けが行なわれることになり、この結果被覆切削チップの工具取り付け孔周辺部の硬質被覆層に対する圧縮応力はきわめて高いものとなるので、特に上部層を構成するＡｌ２Ｏ３−ＺｒＯ２層は、ビッカース硬さ（Ｈｖ）で約２４００の高硬度を有することと相俟って、これに割れが発生し易くなり、これが原因で硬質被覆層に剥離やチッピングが発生するようになるが、図１に概略斜視図で示される通り、前記ウエットブラストに際して、工具取り付け孔周辺部を研磨せず、この部分のＴｉＮ／ＴｉＣＮ研磨材層を残した状態にしておくと、ＴｉＮ／ＴｉＣＮ研磨材層が、低硬度のＴｉＮ研磨材層（Ｈｖ：約１９５０）と高硬度のＴｉＣＮ研磨材層（Ｈｖ：約２６００）との交互積層構造で構成されていることによって、工具本体への被覆切削チップの取り付けに際して、締め付け強度を著しく増大させることができると共に、前記Ａｌ２Ｏ３−ＺｒＯ２層に対する圧縮応力を著しく分散緩和するように作用することから、きわめて強固な固着取り付けが可能となるばかりでなく、前記Ａｌ２Ｏ３−ＺｒＯ２層における剥離やチッピングの原因となる割れの発生が防止されるようになること。
以上（ａ）〜（ｃ）に示される研究結果を得たのである。
(C) As described above, the cutting speed is 350 m / min. In high-speed cutting processing exceeding 1, the load applied to the cutting edge of the coated cutting tip is extremely high. Therefore, especially in the case of milling, the coated cutting tip is attached to the tool body with a very high clamping force. As a result, the compressive stress on the hard coating layer around the tool mounting hole of the coated cutting tip becomes extremely high, and in particular, the Al 2 O 3 —ZrO 2 layer constituting the upper layer is made of Vickers. Combined with having a high hardness (Hv) of about 2400, it is easy for cracks to occur, which causes peeling and chipping on the hard coating layer. As shown in the schematic perspective view, in the wet blasting, the peripheral portion of the tool attachment hole is not polished and the TiN / TiCN abrasive layer of this portion is left. In this case, the TiN / TiCN abrasive layer is composed of an alternately laminated structure of a low hardness TiN abrasive layer (Hv: about 1950) and a high hardness TiCN abrasive layer (Hv: about 2600). Accordingly, when the coated cutting tip is attached to the tool body, the fastening strength can be remarkably increased, and the compressive stress on the Al 2 O 3 —ZrO 2 layer can be remarkably dispersed and relaxed. Not only can the firm attachment be achieved, but also the generation of cracks that cause peeling and chipping in the Al 2 O 3 —ZrO 2 layer is prevented.
The research results shown in (a) to (c) above were obtained.
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、かつ中心部に工具取り付け孔を有するチップ基体の切刃稜線部を含むすくい面および逃げ面の全面に、
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、
上部層として、１〜１５μｍの平均層厚を有し、化学蒸着した状態で、酸化アルミニウムと酸化ジルコニウムの２相混合酸化物組織を有し、かつ、前記酸化ジルコニウムは、Ｚｒの含有割合に換算して、層中に含有するＡｌとＺｒの合量に占める割合（原子比）で、０．０１〜０．２０である、酸化アルミニウムと酸化ジルコニウムの２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）、
で構成された硬質被覆層を蒸着形成してなる、表面被覆サーメット製切削スローアウエイチップにおいて、
上記硬質被覆層の上部層である上記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の全面に、いずれも０．１〜２．５μｍの平均層厚を有する窒化チタン層と炭窒化チタン層の２層以上の交互積層で構成され、かつ、０．４〜５μｍの全体平均層厚を有する研磨材層を蒸着形成した状態で、
ウエットブラストにて、噴射研磨材として、水との合量に占める割合で１５〜６０質量％の酸化アルミニウム微粒を配合した研磨液を噴射し、
上記の研磨材層のウエットブラストによる粉砕化窒化チタン微粒および粉砕化炭窒化チタン微粒と、噴射研磨材としての酸化アルミニウム微粒の共存下で、上記工具取り付け孔周辺部の研磨材層を残して、上記硬質被覆層の上部層を構成する２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面を研磨して、切刃稜線部を含むすくい面および逃げ面の表面粗さを準拠規格ＪＩＳ・Ｂ０６０１−１９９４に基いた測定で、Ｒａ：０．２μｍ以下としてなる、硬質被覆層が高速切削加工で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スローアウエイチップ（被覆切削チップ）に特徴を有するものである。
以下に、この発明の被覆切削チップの硬質被覆層およびＴｉＮ／ＴｉＣＮ研磨材層、さらにウエットブラストで用いられる研磨液のＡｌ2Ｏ3微粒に関して、上記の通りに数値限定した理由を説明する。
（ａ）硬質被覆層
（ａ−１）下部層のＴｉ化合物層
Ｔｉ化合物層は、２相混合酸化物層の下部層として存在し、自身の具備するすぐれた高温強度によって硬質被覆層の高温強度向上に寄与するほか、チップ基体と２相混合酸化物層のいずれにも強固に密着し、よって硬質被覆層のチップ基体に対する密着性を向上させる作用を有するが、その全体平均層厚が３μｍ未満では、前記作用を十分に発揮させることができず、一方その全体平均層厚が２０μｍを越えると、特に高熱発生を伴なう高速切削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、その全体平均層厚を３〜２０μｍと定めた。
（ａ−２）上部層の２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）
酸化アルミニウムと酸化ジルコニウムの２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）からなる上部層は、そのＡｌ成分によって、すぐれた高温硬さと耐熱性を、また、そのＺｒ成分によって、すぐれた高温強度を備え、被覆切削チップの切削性能（耐チッピング性、耐摩耗性）向上に寄与するが、２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）における酸化ジルコニウムの含有割合は、Ｚｒの含有割合に換算して、層中に含有するＡｌとＺｒの合量に占める割合（＝Ｚｒ／（Ａｌ＋Ｚｒ））で、０．０１〜０．２０(但し、原子比）の範囲内のものとする。Ａｌ２Ｏ３−ＺｒＯ２層における酸化ジルコニウムの含有割合を示すこの値が０．０１未満であると、上部層の高温強度の向上の効果が少なく、一方、この値が０．２０を超えると、上部層における酸化アルミニウム量の相対的な減少により高温硬さ、耐熱性の低下が生じ、その結果として耐摩耗性劣化の傾向がみられるので、２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）における酸化ジルコニウムの含有割合（原子比で換算したＺｒ／（Ａｌ＋Ｚｒ）の値）を、上記のとおり、０．０１〜０．２０の範囲内の値とする。
The present invention has been made on the basis of the above research results, and includes a cutting edge ridge portion of a chip base made of a WC-based cemented carbide or TiCN-based cermet and having a tool mounting hole in the center. On the entire surface and flank,
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,
As an upper layer, it has an average layer thickness of 1 to 15 μm, has a two-phase mixed oxide structure of aluminum oxide and zirconium oxide in the state of chemical vapor deposition, and the zirconium oxide is converted into a content ratio of Zr Then, the ratio (atomic ratio) of the total amount of Al and Zr contained in the layer is 0.01 to 0.20, and the two-phase mixed oxide layer of aluminum oxide and zirconium oxide (Al 2 O 3 -ZrO 2 layer),
In the cutting throwaway tip made of surface-covered cermet formed by vapor-depositing a hard coating layer composed of
A titanium nitride layer and a carbon having an average layer thickness of 0.1 to 2.5 μm are formed on the entire surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) which is the upper layer of the hard coating layer. In a state in which an abrasive layer having a total average layer thickness of 0.4 to 5 μm is formed by vapor deposition, which is composed of two or more alternating layers of titanium nitride layers,
In wet blasting, as a spraying abrasive, a polishing liquid containing 15 to 60% by mass of aluminum oxide fine particles in a proportion of the total amount with water is sprayed,
In the presence of pulverized titanium nitride fine particles and pulverized titanium carbonitride fine particles by wet blasting of the above abrasive layer and aluminum oxide fine particles as a spray abrasive, leaving the abrasive layer around the tool mounting hole, The surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) constituting the upper layer of the hard coating layer is polished to comply with the surface roughness of the rake face and flank face including the cutting edge ridge line portion. Surface-coated cermet cutting throwaway tip (coated cutting tip) with a hard coating layer exhibiting excellent chipping resistance in high-speed cutting processing, with Ra: 0.2 μm or less as measured based on JIS B0601-1994 It has the characteristics.
The reason why the hard coating layer and the TiN / TiCN abrasive layer of the coated cutting chip of the present invention and the Al 2 O 3 fine particles of the polishing liquid used in wet blasting are numerically limited as described above will be described below.
(A) Hard coating layer (a-1) Ti compound layer of the lower layer The Ti compound layer exists as a lower layer of the two-phase mixed oxide layer, and the high temperature strength of the hard coating layer by the excellent high temperature strength that it has. In addition to contributing to the improvement, it has a function of firmly adhering to both the chip base and the two-phase mixed oxide layer, thereby improving the adhesion of the hard coating layer to the chip base, but the overall average layer thickness is less than 3 μm However, when the above-mentioned action cannot be fully exhibited, and the overall average layer thickness exceeds 20 μm, it becomes easy to cause thermoplastic deformation particularly in high-speed cutting accompanied by high heat generation, which is a cause of uneven wear. Therefore, the total average layer thickness was determined to be 3 to 20 μm.
(A-2) Two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) as an upper layer
The upper layer composed of a two-phase mixed oxide layer of aluminum oxide and zirconium oxide (Al 2 O 3 —ZrO 2 layer) has excellent high temperature hardness and heat resistance due to its Al component, and also excellent due to its Zr component. High-temperature strength contributes to improving the cutting performance (chipping resistance, wear resistance) of the coated cutting tip, but the content ratio of zirconium oxide in the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) is In terms of the content ratio of Zr, the ratio of the total amount of Al and Zr contained in the layer (= Zr / (Al + Zr)) in the range of 0.01 to 0.20 (however, atomic ratio) Shall be. When this value indicating the content ratio of zirconium oxide in the Al 2 O 3 —ZrO 2 layer is less than 0.01, the effect of improving the high-temperature strength of the upper layer is small, whereas when this value exceeds 0.20 The relative decrease in the amount of aluminum oxide in the upper layer causes a decrease in high-temperature hardness and heat resistance. As a result, there is a tendency for wear resistance to deteriorate, so a two-phase mixed oxide layer (Al 2 O 3 − The content ratio of zirconium oxide in the ZrO 2 layer) (the value of Zr / (Al + Zr) converted in terms of atomic ratio) is set to a value in the range of 0.01 to 0.20 as described above.
また、その平均層厚が１μｍ未満では、所望のすぐれた切削性能を長期に亘って発揮させることができず、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。
（ｂ）ＴｉＮ／ＴｉＣＮ研磨材層
上記の通り、ＴｉＮ／ＴｉＣＮ研磨材層は、ウエットブラスト時に、研磨液に噴射研磨材として配合したＡｌ2Ｏ3微粒によって粉砕微粒化し、ＴｉＮ微粒およびＴｉＣＮ微粒となって前記Ａｌ2Ｏ3微粒との共存下で研磨材として作用し、硬質被覆層の上部層を構成する２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面を研磨するが、この場合、個々の研磨材層の平均層厚が０．１μｍ未満であったり、ＴｉＮ／ＴｉＣＮ研磨材層の全体平均層厚が０．４μｍ未満であったりすると、十分な締め付け強度および前記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）に対する圧縮応力の分散緩和作用を確保することができないばかりでなく、ウエットブラスト時における粉砕化ＴｉＮ微粒および粉砕化ＴｉＣＮ微粒の割合が少な過ぎて、研磨機能を十分に発揮することができず、一方、個々の研磨材層の平均層厚が２．５μｍを越えたり、ＴｉＮ／ＴｉＣＮ研磨材層の全体平均層厚が５μｍを越えたりすると、研磨液に噴射研磨材として配合したＡｌ2Ｏ3微粒とのバランスがくずれて、相対的に多くなり過ぎ、この場合も研磨機能が急激に低下するようになり、いずれの場合も２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面をＲａ：０．２μｍ以下の表面粗さに研磨することができなくなるという理由で、個々の研磨材層の平均層厚を０．１〜２．５μｍ、その全体平均層厚を０．４〜５μｍと定めた。
（ｃ）研磨液のＡｌ2Ｏ3微粒の割合
研磨液のＡｌ2Ｏ3微粒には、ウエットブラスト時にＴｉＮ／ＴｉＣＮ研磨材層の粉砕化ＴｉＮ微粒および粉砕化ＴｉＣＮ微粒と共存した状態で、２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面を研磨する作用があるが、その割合が水との合量に占める割合で１５質量％未満でも、また６０質量％を越えても研磨機能が急激に低下するようになることから、その割合を１５〜６０質量％と定めた。
Further, if the average layer thickness is less than 1 μm, the desired excellent cutting performance cannot be exhibited over a long period of time. On the other hand, if the average layer thickness exceeds 15 μm, chipping is likely to occur. Therefore, the average layer thickness was determined to be 1 to 15 μm.
(B) TiN / TiCN abrasive material layer As described above, the TiN / TiCN abrasive material layer is pulverized and atomized by Al 2 O 3 fine particles blended in the polishing liquid as an injection abrasive during wet blasting, and TiN fine particles and TiCN fine particles It acts as an abrasive in the presence of the Al 2 O 3 fine particles and polishes the surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) constituting the upper layer of the hard coating layer. In this case, if the average layer thickness of each abrasive layer is less than 0.1 μm, or if the overall average layer thickness of the TiN / TiCN abrasive layer is less than 0.4 μm, sufficient clamping strength and 2 Not only cannot the dispersion relaxation effect of compressive stress on the phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) be ensured, but also pulverized TiN fine particles and pulverized during wet blasting The proportion of the TiCN fine particles is too small to fully exhibit the polishing function. On the other hand, the average layer thickness of each abrasive layer exceeds 2.5 μm, or the entire average layer of the TiN / TiCN abrasive layer When the thickness exceeds 5 μm, the balance with the Al 2 O 3 fine particles blended in the polishing liquid as a spray abrasive is lost and becomes relatively large. In this case, the polishing function is rapidly reduced. In any case, the surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) cannot be polished to a surface roughness of Ra: 0.2 μm or less. The average layer thickness was set to 0.1 to 2.5 μm, and the overall average layer thickness was set to 0.4 to 5 μm.
The Al 2 O 3 fine of Al 2 O 3 fine fraction polishing solution of (c) polishing solution, while coexisting with pulverized TiN atomization and pulverization TiCN fine of TiN / TiCN abrasive layer during wet blasting, 2 Although it has an action of polishing the surface of the phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer), even if the ratio is less than 15% by mass in the total amount with water, it also exceeds 60% by mass. However, since the polishing function suddenly decreases, the ratio is determined to be 15 to 60% by mass.
この発明の被覆切削チップは、硬質被覆層の上部層を構成する酸化アルミニウムと酸化ジルコニウムの２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の切刃稜線部を含むすくい面および逃げ面が、Ｒａ：０．２μｍ以下の表面粗さに研磨され、さらに工具取り付け孔周辺部に存在するＴｉＮ／ＴｉＣＮ研磨材層が、工具本体への被覆切削チップの取り付けに際して、高速切削加工では不可欠の高い締め付け力の緩衝層として作用することから、前記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）に対する圧縮応力が著しく小さなものとなり、この結果剥離やチッピング発生の原因となる割れ発生が防止されるようになることと相俟って、各種の鋼や鋳鉄などの切削加工を、切削速度が３５０ｍ／ｍｉｎ．を越える高速で行うのに用いた場合にも、すぐれた耐チッピング性を発揮し、使用寿命の一層の延命化を可能とするものである。 The coated cutting tip of the present invention includes a rake face and a relief including a cutting edge ridge line portion of a two-phase mixed oxide layer of aluminum oxide and zirconium oxide (Al 2 O 3 —ZrO 2 layer) constituting the upper layer of the hard coating layer. The surface is polished to a surface roughness of Ra: 0.2 μm or less, and the TiN / TiCN abrasive layer around the tool mounting hole is indispensable for high-speed cutting when attaching a coated cutting tip to the tool body. Since this acts as a buffer layer with a high clamping force, the compressive stress on the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) becomes extremely small, and as a result, cracks that cause peeling and chipping occur. Combined with the prevention of occurrence, various steels and cast irons are cut at a cutting speed of 350 m / min. Even when used for high-speed operation exceeding the above, excellent chipping resistance is exhibited, and the service life can be further extended.
つぎに、この発明の被覆切削チップを実施例により具体的に説明する。 Next, the coated cutting tip 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、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基超硬合金製のチップ基体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 processing, chip bases A to F made of a WC-based cemented carbide having a throwaway tip shape defined 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、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・ＣＮＭＧ１２０４１２のチップ形状をもったＴｉＣＮ基サーメット製のチップ基体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. TiCN base cermet chip bases a to f having a standard / CNMG12041 chip shape were formed.
ついで、これらのチップ基体Ａ〜Ｆおよびチップ基体ａ〜ｆ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層は特開平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）、表４に示される条件にて、表６に示される目標層厚のＴｉ化合物層およびＡｌ２Ｏ３−ＺｒＯ２層を硬質被覆層の下部層および上部層として蒸着形成し（図３参照）、
ついで、同じく表３に示されるＴｉＮ研磨材層およびＴｉＣＮ研磨材層形成条件でＴｉＮ／ＴｉＣＮ研磨材層を、同じく表７に示される積層数および目標層厚で蒸着形成し（図２参照）、
引き続いて、上記のＴｉＮ／ＴｉＣＮ研磨材層形成の被覆切削チップに、表５に示されるブラスト条件で、かつ表７に示される組み合わせでウエットブラストを施して、工具取り付け孔周辺部にＴｉＮ／ＴｉＣＮ研磨材層を存在させた状態で、前記Ａｌ２Ｏ３−ＺｒＯ２層（上部層）の切刃稜線部を含むすくい面および逃げ面を、同じく表７に示される表面粗さに研磨することにより本発明被覆切削チップ１〜１３をそれぞれ製造した（図１参照）。
Next, each of these chip bases A to F and chip bases a to f is charged into a normal chemical vapor deposition apparatus,
First, Table 3 (the l-TiCN layer in Table 3 shows the conditions for forming a TiCN layer having a vertically elongated crystal structure described in JP-A-6-8010, and the other is a normal granular crystal structure. Under the conditions shown in Table 4, the Ti compound layer and the Al 2 O 3 —ZrO 2 layer having the target layer thickness shown in Table 6 are replaced with the lower layer and the upper layer of the hard coating layer. As a vapor deposition (see FIG. 3),
Next, a TiN / TiCN abrasive layer was formed by vapor deposition with the number of layers and the target layer thickness also shown in Table 7 under the TiN abrasive layer and TiCN abrasive layer formation conditions shown in Table 3 (see FIG. 2).
Subsequently, the coated cutting tip for forming the TiN / TiCN abrasive layer was wet-blasted under the blasting conditions shown in Table 5 and in the combinations shown in Table 7, and TiN / TiCN was formed around the tool mounting hole. The rake face and flank face including the cutting edge ridge line part of the Al 2 O 3 —ZrO 2 layer (upper layer) are polished to the surface roughness shown in Table 7 in the presence of the abrasive layer. According to the present invention, the coated cutting chips 1 to 13 of the present invention were manufactured (see FIG. 1).
また、比較の目的で、表８に示される通り、上記ＴｉＮ／ＴｉＣＮ研磨材層の形成を行なわないで、ウエットブラストを硬質被覆層のＡｌ２Ｏ３−ＺｒＯ２層の表面に直接施す以外は同一の条件で従来被覆切削チップ１〜１３をそれぞれ製造した。 For comparison purposes, as shown in Table 8, except that the TiN / TiCN abrasive layer is not formed and wet blasting is performed directly on the surface of the Al 2 O 3 —ZrO 2 layer of the hard coating layer. Conventionally coated cutting chips 1 to 13 were manufactured under the same conditions.
この結果得られた従来被覆切削チップ１〜１３の硬質被覆層を構成するＡｌ２Ｏ３−ＺｒＯ２層のウエットブラスト後の表面粗さを表８に示した。 Table 8 shows the surface roughness after wet blasting of the Al 2 O 3 —ZrO 2 layer constituting the hard coating layers of the conventional coated cutting chips 1 to 13 obtained as a result.
また、上記本発明被覆切削チップ１〜１３の硬質被覆層および研磨材層の組成、さらに従来被覆切削チップ１〜１３の硬質被覆層の組成を、それぞれ厚さ方向中央部をオージェ分光分析装置で測定したところ、いずれも目標組成と実質的に同じ組成を示し、さらに同構成層の厚さを、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。 In addition, the composition of the hard coating layer and the abrasive layer of the above-described coated cutting chips 1 to 13 of the present invention, and the composition of the hard coating layer of the conventional coated cutting chips 1 to 13 are each measured with an Auger spectroscopic analyzer at the center in the thickness direction. When measured, all showed substantially the same composition as the target composition, and when the thickness of the same constituent layer was measured using a scanning electron microscope (longitudinal section measurement), both were substantially the same as the target layer thickness. The same average layer thickness (average value of 5-point measurement) was shown.
つぎに、上記の本発明被覆切削チップ１〜１３および従来被覆切削チップ１〜１３の各種の被覆切削チップについて、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・ＦＣ３５０の長さ方向等間隔４本縦溝入り丸棒、
切削速度： ５００ ｍ／ｍｉｎ、
切り込み： １．５ ｍｍ、
送り： ０．２０ ｍｍ／ｒｅｖ、
切削時間： ５ 分、
の条件（切削条件Ａという）での普通鋳鉄の乾式断続高速切削試験（通常の切削速度は２００ｍ／ｍｉｎ）、
被削材：ＪＩＳ・Ｓ２０Ｃの長さ方向等間隔４本縦溝入り丸棒、
切削速度： ４８０ ｍ／ｍｉｎ、
切り込み： ３．０ ｍｍ、
送り： ０．３５ ｍｍ／ｒｅｖ、
切削時間： １１ 分、
の条件（切削条件Ｂという）での炭素鋼の乾式断続高速切削試験（通常の切削速度は２００ｍ／ｍｉｎ）、さらに、
被削材：ＪＩＳ・ＳＣＭ４３５の丸棒、
切削速度： ５００ ｍ／ｍｉｎ、
切り込み： １．０ ｍｍ、
送り： ０．２５ ｍｍ／ｒｅｖ、
切削時間： ６ 分、
の条件（切削条件Ｃという）での合金鋼の乾式連続高速切削試験（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９に示した。
Next, for the various coated cutting chips of the present invention coated cutting chips 1 to 13 and the conventional coated cutting chips 1 to 13 described above, all of them are screwed to the tip of the tool steel tool with a fixing jig,
Work material: JIS / FC350 lengthwise equidistant round bars with 4 vertical grooves,
Cutting speed: 500 m / min,
Cutting depth: 1.5 mm,
Feed: 0.20 mm / rev,
Cutting time: 5 minutes,
Dry interrupted high-speed cutting test of normal cast iron under the conditions (cutting condition A) (normal cutting speed is 200 m / min),
Work material: JIS / S20C lengthwise equidistant round bars with 4 vertical grooves,
Cutting speed: 480 m / min,
Cutting depth: 3.0 mm,
Feed: 0.35 mm / rev,
Cutting time: 11 minutes,
Dry intermittent high speed cutting test (normal cutting speed is 200 m / min) of carbon steel under the above conditions (referred to as cutting conditions B),
Work material: JIS / SCM435 round bar,
Cutting speed: 500 m / min,
Cutting depth: 1.0 mm,
Feed: 0.25 mm / rev,
Cutting time: 6 minutes,
The dry continuous high-speed cutting test (normal cutting speed is 200 m / min) of the alloy steel under the above conditions (referred to as cutting condition C) was performed, and the flank wear width of the cutting edge was measured in any cutting test. The measurement results are shown in Table 9.
表６〜９に示される結果から、本発明被覆切削チップ１〜１３は、いずれも硬質被覆層の上部層を構成する２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の切刃稜線部を含むすくい面および逃げ面が、Ｒａ：０．２μｍ以下の表面粗さに研磨され、さらに工具取り付け孔周辺部に存在するＴｉＮ／ＴｉＣＮ研磨材層が、３５０ｍ／ｍｉｎを越える高速切削加工では不可欠の高い締め付け力で、かつ圧縮応力を分散緩和した状態で、工具本体への被覆切削チップの取り付けを可能とすることから、上部層の２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）における剥離やチッピングの原因となる割れ発生が防止され、鋼および鋳鉄の高速切削加工で、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のに対して、硬質被覆層の上部層を構成する２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面粗さが、Ｒａ：０．３〜０．６μｍを示す従来被覆切削チップ１〜１３においては、いずれも３５０ｍ／ｍｉｎを越える高速切削加工では、工具取り付けに高い締め付け力を必要とすることと相俟って、前記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）にチッピングが発生し、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 9, the present coated cutting tips 1 to 13 each have a cutting edge of a two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) constituting the upper layer of the hard coating layer. The rake face and flank face including the ridge line part are polished to a surface roughness of Ra: 0.2 μm or less, and the TiN / TiCN abrasive layer existing around the tool attachment hole has a high-speed cutting process exceeding 350 m / min. In this case, it is possible to attach the coated cutting tip to the tool body with an indispensable high clamping force and in a state where the compressive stress is dispersed and relaxed. Therefore, the upper two-layer mixed oxide layer (Al 2 O 3 —ZrO cracking that causes peeling and chipping in the second layer) is prevented, a high speed cutting of steel and cast iron, shows excellent chipping resistance, whereas exhibit excellent cutting performance over a long period of time, Surface roughness of the two-phase mixed oxide layer constituting the upper layer quality coating layer (Al 2 O 3 -ZrO 2 layer), Ra: 0.3 to 0.6 .mu.m in the conventional coated cutting chips 1-13 showing the In both cases, high-speed cutting exceeding 350 m / min combined with the need for high clamping force for tool attachment, chipping the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer). It is clear that the service life is reached in a relatively short time.
上述のように、この発明の被覆切削チップは、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、特に切削加工を３５０ｍ／ｍｉｎを越えた高速で行う場合に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 cutting tip of the present invention can be used not only for continuous cutting and intermittent cutting under normal conditions such as various steels and cast iron, but also when cutting is performed at a high speed exceeding 350 m / min. Because it shows excellent chipping resistance 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 work, and further cost reduction. Is.
Claims (1)
下部層として、炭化チタン層、窒化チタン層、炭窒化チタン層、炭酸化チタン層、および炭窒酸化チタン層のうちの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、
上部層として、１〜１５μｍの平均層厚を有し、化学蒸着した状態で、酸化アルミニウムと酸化ジルコニウムの２相混合酸化物組織を有し、かつ、前記酸化ジルコニウムは、Ｚｒの含有割合に換算して、層中に含有するＡｌとＺｒの合量に占める割合（原子比）で、０．０１〜０．２０である、酸化アルミニウムと酸化ジルコニウムの２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）、
で構成された硬質被覆層を蒸着形成してなる、表面被覆サーメット製切削スローアウエイチップにおいて、
上記硬質被覆層の上部層である上記２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の全面に、いずれも０．１〜２．５μｍの平均層厚を有する窒化チタン層と炭窒化チタン層の２層以上の交互積層で構成され、かつ、０．４〜５μｍの全体平均層厚を有する研磨材層を蒸着形成した状態で、
ウエットブラストにて、噴射研磨材として、水との合量に占める割合で１５〜６０質量％の酸化アルミニウム微粒を配合した研磨液を噴射し、
上記の研磨材層のウエットブラストによる粉砕化窒化チタン微粒および粉砕化炭窒化チタン微粒と、噴射研磨材としての酸化アルミニウム微粒の共存下で、上記工具取り付け孔周辺部の研磨材層を残して、上記硬質被覆層の上部層を構成する２相混合酸化物層（Ａｌ２Ｏ３−ＺｒＯ２層）の表面を研磨して、切刃稜線部を含むすくい面および逃げ面の表面粗さを準拠規格ＪＩＳ・Ｂ０６０１−１９９４に基いた測定で、Ｒａ：０．２μｍ以下としたことを特徴とする、硬質被覆層が高速切削加工で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スローアウエイチップ。
It is composed of a tungsten carbide base cemented carbide or a titanium carbonitride base cermet, and the entire rake face and flank face including the cutting edge ridge line part of the chip base having a tool attachment hole in the center part,
The lower layer is composed of one or more of a titanium carbide layer, a titanium nitride layer, a titanium carbonitride layer, a titanium carbonate layer, and a titanium carbonitride oxide layer, and has an overall average layer thickness of 3 to 20 μm. Having a Ti compound layer,
As an upper layer, it has an average layer thickness of 1 to 15 μm, has a two-phase mixed oxide structure of aluminum oxide and zirconium oxide in the state of chemical vapor deposition, and the zirconium oxide is converted into a content ratio of Zr Then, the ratio (atomic ratio) of the total amount of Al and Zr contained in the layer is 0.01 to 0.20, and the two-phase mixed oxide layer of aluminum oxide and zirconium oxide (Al 2 O 3 -ZrO 2 layer),
In the cutting throwaway tip made of surface-covered cermet formed by vapor-depositing a hard coating layer composed of
A titanium nitride layer and a carbon having an average layer thickness of 0.1 to 2.5 μm are formed on the entire surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) which is the upper layer of the hard coating layer. In a state in which an abrasive layer having a total average layer thickness of 0.4 to 5 μm is formed by vapor deposition, which is composed of two or more alternating layers of titanium nitride layers,
In wet blasting, as a spraying abrasive, a polishing liquid containing 15 to 60% by mass of aluminum oxide fine particles in a proportion of the total amount with water is sprayed,
In the presence of pulverized titanium nitride fine particles and pulverized titanium carbonitride fine particles by wet blasting of the above abrasive layer and aluminum oxide fine particles as a spray abrasive, leaving the abrasive layer around the tool mounting hole, The surface of the two-phase mixed oxide layer (Al 2 O 3 —ZrO 2 layer) constituting the upper layer of the hard coating layer is polished to comply with the surface roughness of the rake face and flank face including the cutting edge ridge line portion. A surface-coated cermet cutting throwaway tip with a hard coating layer exhibiting excellent chipping resistance in high-speed cutting processing, characterized in that Ra is 0.2 μm or less as measured based on the standard JIS B0601-1994. .
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Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54136489A (en) * | 1978-04-14 | 1979-10-23 | Ngk Spark Plug Co Ltd | Keeper |
| JPH07100701A (en) * | 1993-05-31 | 1995-04-18 | Sumitomo Electric Ind Ltd | Coated cutting tool and its manufacture |
| JPH0852603A (en) * | 1994-07-20 | 1996-02-27 | Sandvik Ab | Cutting tool insert and manufacture thereof |
| JP2001310203A (en) * | 1999-08-12 | 2001-11-06 | Mitsubishi Materials Corp | Surface covered cemented carbide made cutting tool excellent in surface lubricity against chip |
| WO2002004156A1 (en) * | 2000-07-12 | 2002-01-17 | Sumitomo Electric Industries, Ltd. | Coated cutting tool |
| JP2003170311A (en) * | 2001-11-30 | 2003-06-17 | Sumitomo Electric Ind Ltd | Rotary cutting tool and its accessory |
| JP2005212045A (en) * | 2004-01-29 | 2005-08-11 | Kyocera Corp | Holder for cutting tool and cutting tool using this holder |
| JP2005297145A (en) * | 2004-04-13 | 2005-10-27 | Sumitomo Electric Hardmetal Corp | Surface-coated end mill and surface-coated drill |
-
2005
- 2005-12-13 JP JP2005359201A patent/JP4857752B2/en not_active Expired - Fee Related
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54136489A (en) * | 1978-04-14 | 1979-10-23 | Ngk Spark Plug Co Ltd | Keeper |
| JPH07100701A (en) * | 1993-05-31 | 1995-04-18 | Sumitomo Electric Ind Ltd | Coated cutting tool and its manufacture |
| JPH0852603A (en) * | 1994-07-20 | 1996-02-27 | Sandvik Ab | Cutting tool insert and manufacture thereof |
| JP2001310203A (en) * | 1999-08-12 | 2001-11-06 | Mitsubishi Materials Corp | Surface covered cemented carbide made cutting tool excellent in surface lubricity against chip |
| WO2002004156A1 (en) * | 2000-07-12 | 2002-01-17 | Sumitomo Electric Industries, Ltd. | Coated cutting tool |
| JP2003170311A (en) * | 2001-11-30 | 2003-06-17 | Sumitomo Electric Ind Ltd | Rotary cutting tool and its accessory |
| JP2005212045A (en) * | 2004-01-29 | 2005-08-11 | Kyocera Corp | Holder for cutting tool and cutting tool using this holder |
| JP2005297145A (en) * | 2004-04-13 | 2005-10-27 | Sumitomo Electric Hardmetal Corp | Surface-coated end mill and surface-coated drill |
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