JP4857711B2 - Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting - Google Patents
Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting Download PDFInfo
- Publication number
- JP4857711B2 JP4857711B2 JP2005311212A JP2005311212A JP4857711B2 JP 4857711 B2 JP4857711 B2 JP 4857711B2 JP 2005311212 A JP2005311212 A JP 2005311212A JP 2005311212 A JP2005311212 A JP 2005311212A JP 4857711 B2 JP4857711 B2 JP 4857711B2
- Authority
- JP
- Japan
- Prior art keywords
- layer
- cutting
- titanium
- hard coating
- thickness
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Landscapes
- Chemical Vapour Deposition (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Description
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穴なし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）の表面研磨方法に関するものである。 The present invention is a cutting throwaway tip made of a surface-coated cermet without a hole (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 steels and cast irons. ) Surface polishing method .
従来、一般に、図４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た基体（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、
（ａ−１）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、
（ａ−２）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α型の結晶構造を有する酸化アルミニウム層（以下、α型Ａｌ2Ｏ3層で示す）、
以上（ａ−１）および（ａ−２）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いる。
また、上記の被覆切削チップが、図５に概略斜視図で示される通り、工具本体、例えばシャンク部の先端部にシートを介して載置され、チップ上面にクランク駒の先端部を当接させ、前記クランク駒後部に設けたクランプねじの締め込みにより交換自在に挟み締め固定した状態で、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も良く知られている。
Conventionally, in general, as shown in a schematic perspective view in FIG. 4, 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 referred to as these). On the entire surface of the rake face and flank including the cutting edge ridge line portion of the chip base)
(A-1) 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 "TiN"). A Ti compound layer composed of one or more of a layer represented by TiCO) and a titanium carbonitride oxide (hereinafter represented by TiCNO) layer and having an overall average layer thickness of 3 to 20 μm,
(A-2) As an upper layer, an aluminum oxide layer (hereinafter referred to as an α-type Al 2 O 3 layer) having an average layer thickness of 1 to 15 μm and having an α-type crystal structure in a state of chemical vapor deposition,
A coated cutting tip formed by vapor-depositing the hard coating layer constituted by (a-1) and (a-2) is known.
Further, as shown in the schematic perspective view in FIG. 5, the above-mentioned coated cutting tip is placed through a sheet on the tip of the tool body, for example, the shank, and the tip of the crank piece is brought into contact with the upper surface of the tip. It is also well known that, for example, it is used for continuous cutting and intermittent cutting of various steels, cast irons, etc. in a state where the clamp screw provided at the rear of the crank piece is clamped and fixed in a replaceable manner.
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、上記の被覆切削チップの硬質被覆層を構成するα型Ａｌ2Ｏ3層（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。
Furthermore, it is also known that the surface of the α-type Al 2 O 3 layer (upper layer) constituting the hard coating layer of the above-described coated cutting tip is smoothed by wet blasting for the purpose of improving cutting performance. Yes.
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α型Ａｌ2Ｏ3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 equipment 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 be faster. 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 it is used for cutting at a high speed exceeding 1, the α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer is likely to chip (small chipping), and as a result, in a relatively short time. At present, the service life is reached.
そこで、本発明者等は、上述のような観点から、上記のα型Ａｌ2Ｏ3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、特に前記α型Ａｌ2Ｏ3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α型Ａｌ2Ｏ3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α型Ａｌ2Ｏ3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α型Ａｌ2Ｏ3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。
The present inventors have, from the viewpoint as described above, focuses on coated cutting tip α type the Al 2 O 3 layer described above constituting the upper layer of the hard coating layer, in particular the α-type the Al 2 O 3 layer As a result of research to improve chipping resistance of
(A) On the surface of the α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer in the above-mentioned conventional coated cutting chip, the ratio of the wet blasting material to the total amount of water as a spraying abrasive is 15 When the polishing liquid containing -60 mass% aluminum oxide (hereinafter referred to as Al 2 O 3 ) fine particles is sprayed and polished, the α-type Al 2 O 3 layer is based on the compliant standard JIS B0601-1994. (The following surface roughness indicates all measured values based on the standard), and Ra: 0.3-0.6 μm surface roughness is obtained. Even when a coated cutting tip having a surface roughness of Ra: 0.3 to 0.6 μm smoothed by wet blasting on the surface of the 2 O 3 layer was used, 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α型Ａｌ2Ｏ3層の切刃稜線部を含むすくい面および逃げ面の全面に、
（ｂ−１）まず、下側層として、反応ガス組成を、体積％で、
ＴｉＣｌ4：０．２〜１０％、
ＣＯ2：０．１〜１０％、
Ａｒ：５〜６０％、
Ｈ2：残り、
とし、かつ、
反応雰囲気温度：８００〜１１００℃、
反応雰囲気圧力：４〜７０ｋＰａ、
とした条件で、０．１〜３μｍの平均層厚を有し、かつ、オージェ分光分析装置で測定して、Ｔｉに対する酸素の割合が原子比で１．２５〜１．９０、即ち、
組成式：ＴｉＯW 、
で表わした場合、
Ｗ：原子比で１．２５〜１．９０、
を満足する酸化チタン層を化学蒸着形成し、
（ｂ−２）ついで、上記酸化チタン層（下側層）の上に、上側層として、通常の条件、即ち、反応ガス組成を、体積％で、
ＴｉＣｌ4：０．２〜１０％、
Ｎ2：４〜６０％、
Ｈ2：残り、
とし、かつ、
反応雰囲気温度：８００〜１１００℃、
反応雰囲気圧力：４〜９０ｋＰａ、
とした条件で、０．０５〜２μｍの平均層厚を有するＴｉＮ層を化学蒸着形成すると、
（ｂ−３）上記ＴｉＮ層（上側層）形成時に、上記下側層を構成する酸化チタン層の酸素が拡散してきて前記上側層（ＴｉＮ層）が、窒酸化チタン層で構成されるようになるが、この場合上記上側層（前記窒酸化チタン層）形成後の上記下側層である酸化チタン層は、厚さ方向中央部をオージェ分光分析装置で測定して、酸素の割合がＴｉに対する原子比で１．２〜１．７、即ち、
組成式：ＴｉＯX 、
で表わした場合、
Ｘ：原子比で１．２〜１．７、
を満足する酸化チタン層となり、
（ｂ−４）また、上記窒酸化チタン層で構成された上側層は、同じく厚さ方向中央部をオージェ分光分析装置で測定して、拡散酸素の割合が窒素（Ｎ）に対する原子比で０．０１〜０．４、即ち、
組成式：ＴｉＮ1-Y（Ｏ）Y、
で表わした場合（ただし、（Ｏ）は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す）、
Ｙ：原子比で０．０１〜０．４、
を満足する窒酸化チタン層となること。
(B) On the other hand, as shown in the schematic perspective view of FIG. 2, the rake face and clearance including the cutting edge ridge line portion of the α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer in the conventional coated cutting tip described above. On the entire surface,
(B-1) First, as the lower layer, the reaction gas composition is in volume%,
TiCl 4 : 0.2 to 10%,
CO 2 : 0.1 to 10%,
Ar: 5 to 60%,
H 2 : Remaining
And
Reaction atmosphere temperature: 800-1100 ° C.
Reaction atmosphere pressure: 4 to 70 kPa,
And having an average layer thickness of 0.1 to 3 μm and a ratio of oxygen to Ti of 1.25 to 1.90 as measured by an Auger spectrometer,
Composition formula: TiO W ,
In the case of
W: 1.25 to 1.90 in atomic ratio,
A titanium oxide layer satisfying the chemical vapor deposited,
(B-2) Next, on the titanium oxide layer (lower layer), as an upper layer, the normal conditions, that is, the reaction gas composition in volume%,
TiCl 4 : 0.2 to 10%,
N 2 : 4-60%,
H 2 : Remaining
And
Reaction atmosphere temperature: 800-1100 ° C.
Reaction atmosphere pressure: 4 to 90 kPa,
When a TiN layer having an average layer thickness of 0.05 to 2 μm is formed by chemical vapor deposition under the conditions described above,
(B-3) When forming the TiN layer (upper layer), oxygen in the titanium oxide layer constituting the lower layer is diffused so that the upper layer (TiN layer) is composed of a titanium nitride oxide layer. In this case, the titanium oxide layer, which is the lower layer after the formation of the upper layer (the titanium oxynitride layer), is measured by an Auger spectroscopic analyzer at the center in the thickness direction. 1.2 to 1.7 in atomic ratio,
Composition formula: TiO x ,
In the case of
X: 1.2 to 1.7 in atomic ratio,
Titanium oxide layer that satisfies
(B-4) Further, the upper layer composed of the above titanium oxynitride layer was also measured at the center in the thickness direction with an Auger spectroscopic analyzer, and the proportion of diffused oxygen was 0 in terms of atomic ratio with respect to nitrogen (N). .01-0.4, i.e.
Composition formula: TiN 1-Y (O) Y ,
(Where, (O) represents diffused oxygen from the titanium oxide layer as the lower layer when the upper layer is deposited ),
Y: 0.01 to 0.4 in atomic ratio
Titanium nitride oxide layer that satisfies
（ｃ）上記窒酸化チタン層（上側層）および酸化チタン層（下側層）を化学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、前記窒酸化チタン層および酸化チタン層は、前記Ａｌ2Ｏ3微粒によって粉砕微粒化し、窒酸化チタン微粒および酸化チタン微粒となって前記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α型Ａｌ2Ｏ3層の表面を研磨することになり、この結果研磨後の前記α型Ａｌ2Ｏ3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α型Ａｌ2Ｏ3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。
(C) With the titanium nitride oxide layer (upper layer) and the titanium oxide layer (lower layer) formed by chemical vapor deposition,
When a polishing liquid containing 15 to 60% by mass of Al 2 O 3 fine particles as a spraying abrasive in a ratio to the total amount of water is sprayed by wet blasting as in (a) above, the titanium nitride oxide The layer and the titanium oxide layer are pulverized and pulverized by the Al 2 O 3 fine particles, become titanium oxynitride fine particles and titanium oxide fine particles, and act as an abrasive in the presence of the Al 2 O 3 fine particles. will be polishing the surface of the α-type the Al 2 O 3 layer constituting the layer, the surface of the α-type the Al 2 O 3 layer after the results polishing, Ra: smooth to a surface roughness of not more than 0.2μm When the surface of the α-type Al 2 O 3 layer, which is the upper layer, is smoothed to a surface roughness of Ra: 0.2 μm or less, and high-speed cutting is performed 350 m / 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.
（ｄ）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、きわめて高い挟み締め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クランプ駒当接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ばかりでなく、これに対応して、切削加工時にクランプ駒当接部における機械的震動はきわめて強力なものとなるので、特に上部層を構成するα型Ａｌ2Ｏ3層は、ビッカース硬さ（Ｈｖ）で約３０００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、クランプ駒当接部周辺部を研磨せず、この部分の研磨材層を残した状態にしておくと、上記の研磨材層を構成する窒酸化チタン層（上側層）および酸化チタン層（下側層）は、いずれも前記α型Ａｌ2Ｏ3層に比して、相対的にきわめて低いＨｖ：約２０００の硬さをもつほか、高強度を具備するものであるため、図３に概略斜視図で示される通り、工具本体へのクランプ駒による被覆切削チップの取り付けに際して、高い挟み締め力の緩衝層として作用し、この結果前記α型Ａｌ2Ｏ3層に対する圧縮応力を著しく緩和し、さらに、切削加工時に発生する強力な機械的震動の前記クランプ駒への伝達を吸収し、緩和する防震層としても作用し、これによって前記α型Ａｌ2Ｏ3層に対する前記クランプ駒による震動攻撃が緩和されることから、前記α型Ａｌ2Ｏ3層における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。
以上（ａ）〜（ｄ）に示される研究結果を得たのである。
(D) As described above, the cutting speed is 350 m / min. In high-speed cutting that exceeds 1, the load applied to the cutting edge of the coated cutting tip becomes extremely high. Especially in the case of milling, when attaching the coated cutting tip to the tool body, the clamping force is extremely high. As a result, not only the compressive stress on the hard coating layer of the clamp piece abutting portion of the coated cutting tip is extremely high, but also the clamp piece abutting portion during cutting is correspondingly applied. In particular, the α-type Al 2 O 3 layer constituting the upper layer has a high hardness of about 3000 in terms of Vickers hardness (Hv). Cracks are likely to occur, and this causes peeling and chipping of the hard coating layer. As shown in the schematic perspective view of FIG. At this time, if the peripheral portion of the clamp piece abutting portion is not polished and the abrasive layer of this portion is left, the titanium nitride oxide layer (upper layer) and the titanium oxide layer ( The lower layer) has a relatively very low Hv: hardness of about 2000 as compared with the α-type Al 2 O 3 layer, and has a high strength. As shown in the schematic perspective view, when the coated cutting tip is attached to the tool body with the clamp piece, it acts as a buffer layer with a high clamping force, and as a result, the compressive stress on the α-type Al 2 O 3 layer is remarkably relieved. Furthermore, it acts as a vibration-proof layer that absorbs and relieves the transmission of strong mechanical vibration generated during cutting to the clamp piece, thereby causing a vibration attack by the clamp piece to the α-type Al 2 O 3 layer. Is relaxed From, so cracks occurred to cause peeling and chipping in the α-type Al 2 O 3 layer is prevented and.
The research results shown in (a) to (d) 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た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、
（ａ−１）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、
（ａ−２）上部層として、１〜１５μｍの平均層厚を有するα型Ａｌ2Ｏ3層、
以上（ａ−１）および（ａ−２）で構成された硬質被覆層を化学蒸着形成してなり、かつ、工具本体にクランプ駒による挟み締めにより交換自在に取り付けられる被覆切削チップの表面研磨方法にして、
（１）上記硬質被覆層の上部層であるα型Ａｌ2Ｏ3層の全面に、
（ｂ−１）下側層として、０．１〜３μｍの平均層厚を有し、かつ、
組成式：ＴｉＯX 、
で表わした場合、厚さ方向中央部をオージェ分光分析装置で測定して、
Ｘ：原子比で１．２〜１．７、
を満足する酸化チタン層、
（ｂ−２）上側層として、０．０５〜２μｍの平均層厚を有し、かつ、
組成式：ＴｉＮ1-Y（Ｏ）Y、
で表わした場合（ただし、（Ｏ）は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す）、同じく厚さ方向中央部をオージェ分光分析装置で測定して、
Ｙ：原子比で０．０１〜０．４、
を満足する窒酸化チタン層、
以上（ｂ−１）および（ｂ−２）で構成された研磨材層を化学蒸着形成し、
（２）ついで、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Ａｌ2Ｏ3微粒を配合した研磨液を噴射し、
上記の研磨材層が噴射研磨材であるＡｌ 2 Ｏ 3 微粒の噴射により粉砕微粒化してなる粉砕化酸化チタン微粒（下側層）および粉砕化窒酸化チタン微粒（上側層）と、噴射研磨材としてのＡｌ2Ｏ3微粒の共存下で、上記クランプ駒当接部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α型Ａｌ2Ｏ3層の表面を研磨して、前記α型Ａｌ 2 Ｏ 3 層の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被覆切削チップの表面研磨方法に特徴を有するものである。
The present invention has been made based on the above research results, and the entire rake face and flank face including the cutting edge ridge line portion of the chip base composed of the WC-based cemented carbide or TiCN-based cermet,
(A-1) 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 ,
(A-2) α-type Al 2 O 3 layer having an average layer thickness of 1 to 15 μm as an upper layer,
Surface polishing method for coated cutting tip formed by chemical vapor deposition of hard coating layer composed of (a-1) and (a-2) and attached to the tool body by clamping with a clamp piece so as to be replaceable In
( 1 ) On the entire surface of the α-type Al 2 O 3 layer, which is the upper layer of the hard coating layer,
(B-1) The lower layer has an average layer thickness of 0.1 to 3 μm, and
Composition formula: TiO x ,
, Measure the central part in the thickness direction with an Auger spectrometer,
X: 1.2 to 1.7 in atomic ratio,
Satisfying titanium oxide layer,
(B-2) The upper layer has an average layer thickness of 0.05 to 2 μm, and
Composition formula: TiN 1-Y (O) Y ,
(However, (O) indicates the diffused oxygen from the titanium oxide layer, which is the lower layer when the upper layer is formed by vapor deposition ). Similarly, the central portion in the thickness direction is measured with an Auger spectrometer. ,
Y: 0.01 to 0.4 in atomic ratio
Satisfying titanium oxynitride layer,
Abrasive material layer composed of (b-1) and (b-2) above is formed by chemical vapor deposition,
( 2 ) Next , in wet blasting, as a spraying abrasive, a polishing liquid containing 15 to 60% by mass of Al 2 O 3 fine particles in a proportion of the total amount with water is sprayed.
Abrasive titanium oxide fine particles (lower layer) and pulverized titanium oxynitride fine particles (upper layer) formed by pulverizing and atomizing the above-mentioned abrasive layer by spraying Al 2 O 3 fine particles, which are spray abrasives, and jet abrasives The surface of the α-type Al 2 O 3 layer that constitutes the upper layer of the hard coating layer is polished in the presence of Al 2 O 3 fine particles, leaving an abrasive layer around the clamp piece contact portion. The surface roughness of the rake face and the flank face including the cutting edge ridge line portion of the α-type Al 2 O 3 layer is measured based on JIS / B0601-1994, and Ra: 0.2 μm or less. The coating layer has a feature in the surface polishing method of a coated cutting tip that exhibits excellent chipping resistance in high-speed cutting.
以下に、この発明の被覆切削チップの表面研磨方法において、硬質被覆層および研磨材層、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、α型Ａｌ2Ｏ3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α型Ａｌ2Ｏ3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。
Hereinafter, in the surface polishing method of the coated cutting tip of the present invention, the reason why the hard coating layer, the abrasive layer, 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. .
(A) Hard coating layer (a-1) Ti compound layer of lower layer The Ti compound layer exists as a lower layer of the α-type Al 2 O 3 layer, and the high temperature strength of the hard coating layer is high due to its excellent high-temperature strength. In addition to contributing to strength improvement, it has a function of firmly adhering to both the chip base and the α-type Al 2 O 3 layer, thereby improving the adhesion of the hard coating layer to the chip base, but the overall average layer thickness is If the thickness is less than 3 μm, the above-mentioned effect cannot be sufficiently exerted. On the other hand, if the total average layer thickness exceeds 20 μm, it becomes easy to cause thermoplastic deformation particularly in high-speed cutting accompanied by generation of high heat. Since it becomes a cause, the whole average layer thickness was set to 3-20 micrometers.
（ａ−２）上部層のα型Ａｌ2Ｏ3層
上記のα型Ａｌ2Ｏ3層は、すぐれた高温硬さと耐熱性を有し、被覆切削チップの切削性能向上に寄与するが、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。
(A-2) α-type Al 2 O 3 layer of the upper layer The α-type Al 2 O 3 layer has excellent high-temperature hardness and heat resistance, and contributes to improving the cutting performance of the coated cutting tip. 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 tends to occur. The average layer thickness was set to 1 to 15 μm.
（ｂ）研磨材層
上側層を構成する窒酸化チタン層は、上記の通り、まず、酸素の割合をＮに対する原子比で１．２５〜１．９０（Ｗ値）とした酸化チタン層を形成し、ついで、前記酸化チタン層の上に通常の条件でＴｉＮ層を蒸着することにより形成されるものであり、したがって前記ＴｉＮ層形成時における前記酸化チタン層からの酸素の拡散が不可欠となるが、前記酸化チタン層のＷ値が１．２５未満であると、前記ＴｉＮ層への酸素の拡散反応が急激に低下し、上側層における拡散酸素の割合（Ｙ値）を原子比で０．０１以上にすることができず、一方同Ｗ値が１．９０を越えると、前記上側層における拡散酸素の割合（Ｙ値）が原子比で０．４０を越えて多くなってしまうことから、Ｗ値を１．２５〜１．９０と定めたものであり、この場合上側層形成後の下側層（酸化チタン層）における酸素の割合（Ｘ値）は原子比で１．２〜１．７の範囲内の値をとるようになる、言い換えれば上側層形成後の下側層のＸ値が１．２〜１．７を満足する場合に、前記上側層のＹ値は０．０１〜０．４０を満足するものとなる。
また、この場合、下側層のＸ値および上側層のＹ値をそれぞれ１．２〜１．７および０．０１〜０．４０と定めたのは、前記Ｘ値およびＹ値が前記の値をとった場合に、これら研磨材層のウエットブラスト時における粉砕微粒化が好適な状態で行なわれ、すぐれた研磨機能を十分に発揮することが多くの試験結果から得られ、これらの試験結果に基いて定めたものである。したがって、前記Ｘ値およびＹ値がそれぞれ１．２〜１．７および０．０１〜０．４０の範囲から外れると、前記研磨材層のウエットブラスト時における粉砕微粒化が満足に行なわれず、すぐれた研磨機能を期待することができない。
さらに、上側層および下側層の平均層厚を、それぞれ０．０５〜２μｍおよび０．１〜３μｍとしたのは、その平均層厚が０．０５μｍ未満および０．１μｍ未満では、ウエットブラスト時における下側層の粉砕化酸化チタン微粒、上側層の粉砕化窒酸化チタン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、その平均層厚がそれぞれ２μｍおよび３μｍを越えても、研磨機能が急激に低下するようになり、いずれの場合もα型Ａｌ2Ｏ3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にもとづくものである。
また、平均層厚に関して、上記上側層と下側層の合計平均層厚を０．１μｍ以上としたのは、０．１μｍ未満ではクランプ駒当接面部分の研磨材層による挟み締め力緩衝効果および防震効果を十分に発揮することができないという理由にもよるものである。
(B) Abrasive material layer As described above, the titanium oxynitride layer constituting the upper layer first forms a titanium oxide layer in which the oxygen ratio is 1.25 to 1.90 (W value) in terms of the atomic ratio to N. Then, it is formed by depositing a TiN layer on the titanium oxide layer under normal conditions. Therefore, diffusion of oxygen from the titanium oxide layer during the formation of the TiN layer is indispensable. When the W value of the titanium oxide layer is less than 1.25, the diffusion reaction of oxygen into the TiN layer is drastically reduced, and the ratio of diffused oxygen (Y value) in the upper layer is 0.01 by atomic ratio. On the other hand, if the same W value exceeds 1.90, the ratio of diffused oxygen (Y value) in the upper layer will increase beyond 0.40 in terms of atomic ratio. The value is defined as 1.25 to 1.90, In this case, the oxygen ratio (X value) in the lower layer (titanium oxide layer) after the upper layer formation takes an atomic ratio in the range of 1.2 to 1.7, in other words, the upper layer formation. When the X value of the later lower layer satisfies 1.2 to 1.7, the Y value of the upper layer satisfies 0.01 to 0.40.
In this case, the X value of the lower layer and the Y value of the upper layer are set to 1.2 to 1.7 and 0.01 to 0.40, respectively. It is obtained from many test results that these abrasive layers are pulverized and atomized in a suitable state at the time of wet blasting, and exhibit an excellent polishing function sufficiently. Based on this. Therefore, if the X value and Y value are out of the range of 1.2 to 1.7 and 0.01 to 0.40, respectively, the pulverization and atomization at the time of wet blasting of the abrasive layer is not satisfactorily performed, which is excellent. The polishing function cannot be expected.
Further, the average layer thicknesses of the upper layer and the lower layer were set to 0.05 to 2 μm and 0.1 to 3 μm, respectively, when the average layer thickness was less than 0.05 μm and less than 0.1 μm. The ratio of the pulverized titanium oxide fine particles in the lower layer and the fine pulverized titanium oxynitride fine particles in the upper layer is too small to perform the polishing function sufficiently, while the average layer thickness is 2 μm and 3 μm, respectively. The reason is that the polishing function suddenly deteriorates even if the thickness exceeds the range, and in any case, the surface of the α-type Al 2 O 3 layer cannot be polished to a surface roughness of Ra: 0.2 μm or less. It is based.
Further, regarding the average layer thickness, the total average layer thickness of the upper layer and the lower layer is set to 0.1 μm or more. When the average layer thickness is less than 0.1 μm, the clamping force buffering effect by the abrasive layer on the clamp piece contact surface portion This is also due to the reason that the seismic effect cannot be fully exhibited.
（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研磨材層を構成する下側層の粉砕化酸化チタン微粒および上側層の粉砕化窒酸化チタン微粒と共存した状態で、α型Ａｌ2Ｏ3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。
(C) The Al 2 O 3 fine of Al 2 O 3 fine fraction polishing liquid of the polishing liquid, pulverization oxynitride of pulverized titanium oxide fine and the upper layer of the lower layer of the abrasive layer during wet blasting The surface of the α-type Al 2 O 3 layer is polished while coexisting with the titanium fine particles, but the proportion of the total amount with water is less than 15% by mass or more than 60% by mass. However, since the polishing function suddenly decreases, the ratio is determined to be 15 to 60% by mass.
この発明の方法で表面研磨された被覆切削チップは、硬質被覆層の上部層を構成するα型Ａｌ2Ｏ3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、さらにクランプ駒当接部周辺部に存在する研磨材層が、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挟み締め力の緩衝層として作用するほか、切削加工時に発生する強力な機械的震動の防震層として作用することから、前記α型Ａｌ2Ｏ3層に対する圧縮応力が著しく緩和され、かつ、前記クランプ駒による震動攻撃がきわめて小さなものとなり、この結果前記α型Ａｌ2Ｏ3層における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。 In the coated cutting tip surface-polished by the method of the present invention, the rake face and flank face including the cutting edge ridge portion of the α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer have a Ra: 0.2 μm or less. is polished to a surface roughness of the abrasive layer further present in the clamping piece abutting portion periphery, when coated cutting tip attachment of the tool body, it acts as a buffer layer of clamping force scissors highly essential in high-speed cutting machining In addition, since it acts as an anti-vibration layer for strong mechanical vibration generated during cutting, the compressive stress on the α-type Al 2 O 3 layer is remarkably relieved, and the vibration attack by the clamp piece is extremely small next, it results the α-type Al 2 O 3 cooperation with and be like crack is prevented to cause peeling and chipping in the layer, the cutting of various kinds of steel and cast iron, switching Speed is 350m / 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の表面研磨方法を実施例により具体的に説明する。 Next, the method for polishing the surface of the coated cutting tip according to 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・ＣＮＭＮ１２０４０８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 specified in ISO · CNMN120408 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・ＣＮＭＮ１２０４１２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. Chip bases a to f made of TiCN base cermet having standard / CNMN12041 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化合物層およびα型Ａｌ2Ｏ3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４参照）、
ついで、研磨材層の下側層形成用酸化チタン層［ＴｉＯＷ（１）〜（６）のいずれか］を表４に示される条件で形成した後、上側層形成用窒化チタン層（ＴｉＮ層）を同じく表３に示される条件で、表６に示される目標層厚で蒸着形成して、表６に示される組成、すなわち厚さ方向中央部をオージェ分光分析装置で測定して、それぞれ表６に示されるＸ値およびＹ値の下側層および上側層からなる研磨材層を形成し（図２参照）、
引き続いて、上記の下側層および上側層からなる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６に示される組み合わせでウエットブラストを施して、クランプ駒当接面部分に研磨材層を存在させた状態で、前記α型Ａｌ2Ｏ3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６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 (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 and α-type Al 2 O 3 layer having the target layer thicknesses shown in Table 6 are vapor-deposited as the lower layer and the upper layer of the hard coating layer under the conditions shown in FIG. (See Fig. 4)
Next, after forming the lower layer forming titanium oxide layer [any of TiO W (1) to (6)] under the conditions shown in Table 4, the upper layer forming titanium nitride layer (TiN layer) ) Under the same conditions as shown in Table 3, and with the target layer thickness shown in Table 6, the composition shown in Table 6, that is, the central portion in the thickness direction was measured with an Auger spectroscopic analyzer. Forming an abrasive layer composed of a lower layer and an upper layer of the X value and Y value shown in FIG.
Subsequently, the coated cutting tips for forming the abrasive layer composed of the lower layer and the upper layer are subjected to wet blasting under the blasting conditions shown in Table 5 and the combinations shown in Table 6, The rake face and flank face including the cutting edge ridge line portion of the α-type Al 2 O 3 layer (upper layer) are polished to the surface roughness shown in Table 6 with the abrasive layer present on the surface portion. By doing this, this invention coated cutting tip 1-13 was manufactured, respectively (refer FIG. 1).
また、比較の目的で、表７に示される通り、下側層および上側層からなる研磨材層の形成を行なわない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（図４参照）。
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α型Ａｌ2Ｏ3層のウエットブラスト後の表面粗さを表７に示した。
For comparison purposes, as shown in Table 7, conventionally coated cutting chips 1 to 13 were produced under the same conditions except that the abrasive layer composed of the lower layer and the upper layer was not formed (FIG. 4). reference).
Table 7 shows the surface roughness after wet blasting of the α-type Al 2 O 3 layer constituting the hard coating layer 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および従来被覆切削チップ１〜１３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（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。 Moreover, when the thickness of the constituent layer of the hard coating layer of the present invention coated cutting chips 1 to 13 and the conventional coated cutting chips 1 to 13 was measured using a scanning electron microscope (longitudinal cross section measurement), both were 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、それぞれ図３，５に示される通り、いずれも工具鋼製バイト（工具本体）のシャンク先端部にクランプ駒のクランプねじによる挟み締めにより取り付けた状態で、
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：３５０ｍ／ｍｉｎ、
切り込み：１．５ｍｍ、
送り：０．３ｍｍ／ｒｅｖ、
切削時間：８分、
の条件（切削条件Ａという）での合金鋼の乾式断続高速切削試験（通常の切削速度は１８０ｍ／ｍｉｎ）、
被削材：ＪＩＳ・Ｓ４５Ｃの丸棒、
切削速度：５００ｍ／ｍｉｎ、
切り込み：１ｍｍ、
送り：０．２ｍｍ／ｒｅｖ、
切削時間：５分、
の条件（切削条件Ｂという）での炭素鋼の湿式連続高速切削試験（通常の切削速度は３００ｍ／ｍｉｎ）、さらに、
被削材：ＪＩＳ・ＦＣ３００の丸棒、
切削速度：５００ｍ／ｍｉｎ、
切り込み：２．５ｍｍ、
送り：０．３ｍｍ／ｒｅｖ、
切削時間：１５分、
の条件（切削条件Ｃという）での鋳鉄の湿式連続高速切削試験（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, as for the various coated cutting tips of the present invention coated cutting tips 1 to 13 and the conventional coated cutting tips 1 to 13, respectively, as shown in FIGS. In a state where it is attached to the tip of the shank by clamping with the clamp screw of the clamp piece,
Work material: JIS · SCM440 lengthwise equidistant 4 vertical grooved round bar,
Cutting speed: 350 m / min,
Incision: 1.5mm,
Feed: 0.3mm / rev,
Cutting time: 8 minutes
Dry interrupted high-speed cutting test (normal cutting speed is 180 m / min) of alloy steel under the following conditions (referred to as cutting condition A),
Work material: JIS / S45C round bar,
Cutting speed: 500 m / min,
Cutting depth: 1mm,
Feed: 0.2mm / rev,
Cutting time: 5 minutes
Wet continuous high-speed cutting test (normal cutting speed is 300 m / min) of carbon steel under the conditions (referred to as cutting conditions B),
Work material: JIS / FC300 round bar,
Cutting speed: 500 m / min,
Incision: 2.5mm,
Feed: 0.3mm / rev,
Cutting time: 15 minutes,
A wet continuous high-speed cutting test (normal cutting speed is 250 m / min) of cast iron under the above conditions (referred to as cutting condition C), and the flank wear width of the cutting edge was measured in any cutting test. The measurement results are shown in Table 8.
表６〜８に示される結果から、この発明によって表面研磨された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α型Ａｌ2Ｏ3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、さらにクランプ駒当接面部分に存在する研磨材層が、工具本体への被覆切削チップの取り付けに際しては、３５０ｍ／ｍｉｎを越える高速切削加工では不可欠の高い挟み締め力の緩衝層として作用し、さらに切削加工時に発生する強力な機械的震動の防震層としても作用することから、前記α型Ａｌ2Ｏ3層に対する圧縮応力が著しく緩和され、かつ、前記クランプ駒による震動攻撃がきわめて小さなものとなり、この結果前記α型Ａｌ2Ｏ3層における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、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α型Ａｌ2Ｏ3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挟み締め力を必要とすることと相俟って、前記α型Ａｌ2Ｏ3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 8, the coated cutting tips 1 to 13 of the present invention whose surfaces were polished according to the present invention are all the cutting edge ridges of the α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer. The rake face and the flank face are polished to a surface roughness of Ra: 0.2 μm or less, and the abrasive layer present on the clamp piece abutting surface portion is attached when the coated cutting tip is attached to the tool body. acts as a buffer layer of clamping force scissors highly essential in high-speed cutting of over 350 meters / min, since it also acts as BoShin layer of strong mechanical vibration generated further during cutting, the α-type Al 2 O 3 compressive stress to the layer is remarkably relaxed, and vibration attack becomes extremely small due to the clamping piece, causing peeling and chipping in this that said α-type the Al 2 O 3 layer cracks Raw is prevented, a high speed cutting of steel and cast iron, excellent chipping resistance indicates, with respect to exhibit excellent cutting performance over a long period of time, type α constituting the upper layer of the hard coating layer Al In the conventional coated cutting tips 1 to 13 where the surface roughness of the 2 O 3 layer is Ra: 0.3 to 0.6 μm, high clamping force is required for tool attachment in high-speed cutting that exceeds 350 m / min. It is clear that chipping occurs in the α-type Al 2 O 3 layer in combination with the necessity of the above, and the service life is reached in a relatively short time.
上述のように、この発明の方法によって表面研磨された本発明被覆切削チップは、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, which has been surface-polished by the method of the present invention, has a cutting speed of 350 m / min, in addition to continuous cutting and intermittent cutting under normal conditions such as various steels and cast iron. It exhibits excellent chipping resistance even when performed at high speeds exceeding it, and exhibits excellent cutting performance over a long period of time. It can cope with cost reduction sufficiently.
Claims (1)
（ａ−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、
（ａ−２）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α型の結晶構造を有する酸化アルミニウム層、
以上（ａ−１）および（ａ−２）で構成された硬質被覆層を化学蒸着形成してなり、かつ、工具本体にクランプ駒による挟み締めにより交換自在に取り付けられる穴なし表面被覆サーメット製切削スローアウエイチップの表面研磨方法にして、
（１）上記硬質被覆層の上部層である酸化アルミニウム層の全面に、
（ｂ−１）下側層として、０．１〜３μｍの平均層厚を有し、かつ、
組成式：ＴｉＯX 、
で表わした場合、厚さ方向中央部をオージェ分光分析装置で測定して、原子比で、
Ｘ：１．２〜１．７、
を満足する酸化チタン層、
（ｂ−２）上側層として、０．０５〜２μｍの平均層厚を有し、かつ、
組成式：ＴｉＮ1-Y（Ｏ）Y、
で表わした場合（ただし、（Ｏ）は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す）、同じく厚さ方向中央部をオージェ分光分析装置で測定して、同じく原子比で、
Ｙ：０．０１〜０．４、
を満足する窒酸化チタン層、
以上（ｂ−１）および（ｂ−２）で構成された研磨材層を化学蒸着形成し、
（２）ついで、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、
上記の研磨材層が噴射研磨材である酸化アルミニウム微粒の噴射により粉砕微粒化してなる粉砕化酸化チタン微粒（下側層）および粉砕化窒酸化チタン微粒（上側層）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、上記クランプ駒当接部周辺部の上記研磨材層を残して、上記硬質被覆層の上部層を構成する酸化アルミニウム層の表面を研磨して、前記酸化アルミニウム層の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穴なし表面被覆サーメット製切削スローアウエイチップの表面研磨方法。 On the entire rake face and flank face including the cutting edge ridge line portion of the chip base composed of tungsten carbide base cemented carbide or titanium carbonitride base cermet,
(A-1) 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 a thickness of 3 to 20 μm. A Ti compound layer having an overall average layer thickness,
(A-2) As an upper layer, an aluminum oxide layer having an average layer thickness of 1 to 15 μm and having an α-type crystal structure in a state of chemical vapor deposition,
Surface-covered cermet cutting without holes, which is formed by chemical vapor deposition of the hard coating layer composed of (a-1) and (a-2) and is attached to the tool body by clamping with a clamp piece so as to be replaceable In the surface polishing method of the throwaway tip,
( 1 ) On the entire surface of the aluminum oxide layer that is the upper layer of the hard coating layer,
(B-1) The lower layer has an average layer thickness of 0.1 to 3 μm, and
Composition formula: TiO x ,
, The central part in the thickness direction is measured with an Auger spectrometer, and the atomic ratio is
X: 1.2 to 1.7,
Satisfying titanium oxide layer,
(B-2) The upper layer has an average layer thickness of 0.05 to 2 μm, and
Composition formula: TiN 1-Y (O) Y ,
(However, (O) indicates the diffused oxygen from the titanium oxide layer, which is the lower layer when the upper layer is formed by vapor deposition ). Similarly, the central portion in the thickness direction is measured with an Auger spectrometer. , Also in atomic ratio,
Y: 0.01 to 0.4
Satisfying titanium oxynitride layer,
Abrasive material layer composed of (b-1) and (b-2) above is formed by chemical vapor deposition,
( 2 ) Next , with wet blasting, as a spray 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.
The above-mentioned abrasive material layer is pulverized titanium oxide fine particles (lower layer) and pulverized titanium oxynitride fine particles (upper layer) formed by pulverization and atomization by injection of aluminum oxide fine particles, which are spray abrasives . In the presence of aluminum oxide fine particles, the surface of the aluminum oxide layer constituting the upper layer of the hard coating layer is polished, leaving the abrasive layer around the clamp piece contact portion , and the aluminum oxide layer The hard coating layer has a high-speed cutting process, characterized in that the surface roughness of the rake face and the flank face including the cutting edge ridge line portion is Ra: 0.2 μm or less as measured based on JIS / B0601-1994. A surface polishing method for cutting throwaway tips made of surface-coated cermets without holes that exhibits excellent chipping resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005311212A JP4857711B2 (en) | 2005-10-26 | 2005-10-26 | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005311212A JP4857711B2 (en) | 2005-10-26 | 2005-10-26 | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2007118107A JP2007118107A (en) | 2007-05-17 |
| JP4857711B2 true JP4857711B2 (en) | 2012-01-18 |
Family
ID=38142499
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2005311212A Active JP4857711B2 (en) | 2005-10-26 | 2005-10-26 | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4857711B2 (en) |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114714261B (en) * | 2022-04-15 | 2022-12-27 | 江南大学 | Abrasive water jet nozzle for strengthening |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54136489A (en) * | 1978-04-14 | 1979-10-23 | Ngk Spark Plug Co Ltd | Keeper |
| SE509201C2 (en) * | 1994-07-20 | 1998-12-14 | Sandvik Ab | Aluminum oxide coated tool |
| JP3989664B2 (en) * | 1999-04-13 | 2007-10-10 | 三菱マテリアル株式会社 | Slow-away tip made of surface-coated cemented carbide with excellent chipping resistance |
| JP3893804B2 (en) * | 1999-07-16 | 2007-03-14 | 三菱マテリアル株式会社 | Surface coated cemented carbide cutting tools with excellent chipping resistance |
| WO2002004156A1 (en) * | 2000-07-12 | 2002-01-17 | Sumitomo Electric Industries, Ltd. | Coated cutting tool |
| JP4019246B2 (en) * | 2000-09-04 | 2007-12-12 | 三菱マテリアル株式会社 | Surface coated cemented carbide cutting tools with excellent chipping resistance |
| JP2003170311A (en) * | 2001-11-30 | 2003-06-17 | Sumitomo Electric Ind Ltd | Rotary cutting tool and its accessory |
| JP4360620B2 (en) * | 2004-01-29 | 2009-11-11 | 京セラ株式会社 | Cutting tool holder and cutting tool using the same |
-
2005
- 2005-10-26 JP JP2005311212A patent/JP4857711B2/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| JP2007118107A (en) | 2007-05-17 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4857711B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4849376B2 (en) | Manufacturing method of surface-coated cermet cutting tool that exhibits excellent chipping resistance in high-speed cutting of difficult-to-cut materials | |
| JP4857751B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4853612B2 (en) | Manufacturing method of cutting throwaway tip made of surface coated cermet whose hard coating layer exhibits excellent chipping resistance in high speed cutting | |
| JP4853822B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4900653B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP2007118155A (en) | Surface-coated cermet throwaway cutting tip having hard coating layer exhibiting excellent chipping resistance in high speed cutting | |
| JP4888689B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4900652B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP4883389B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4853621B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP2007118108A (en) | Non-hole surface-coated cermet throwaway cutting tip having hard coating layer exhibiting excellent chipping resistance in high speed cutting | |
| JP4873289B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4888762B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP4888759B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP4888688B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP4853820B2 (en) | Surface polishing method for throated surface-coated cermet with a hard coating layer that exhibits excellent chipping resistance in high-speed cutting | |
| JP4857752B2 (en) | Surface polishing method for cutting throwaway tip made of surface-covered cermet whose hard coating layer exhibits excellent chipping resistance in high-speed cutting | |
| JP4853613B2 (en) | Manufacturing method of cutting throwaway tip made of surface coated cermet whose hard coating layer exhibits excellent chipping resistance in high speed cutting | |
| JP2007111814A (en) | Throwaway cutting tip of surface-coated cermet with hard coating layer achieving excellent anti-chipping performance in high-speed cutting work | |
| JP4857705B2 (en) | Surface polishing method for surface-coated cermet cutting throwaway tips with hard coating layer providing excellent chipping resistance in high-speed cutting | |
| JP2007090457A (en) | Surface coated cermet-made cutting throw-away tip having hard coating layer exhibiting excellent chipping resistance in high speed cutting | |
| JP2007125661A (en) | Non-perforated surface coated cermet-made cutting throw-away chip having hard coated layer exhibiting excellent chipping resistance in high-speed cutting | |
| JP2007118157A (en) | Non-hole surface-coated cermet throwaway cutting tip having hard coating layer exhibiting excellent chipping resistance in high speed cutting | |
| JP2007090455A (en) | Surface coated cermet-made cutting throw-away tip having hard coating layer exhibiting excellent chipping resistance in high speed cutting |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20080321 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20110425 |
|
| A521 | Written amendment |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20110615 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20111004 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20111017 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4857711 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20141111 Year of fee payment: 3 |