JP3353675B2 - Surface-coated cemented carbide cutting tool with excellent chipping resistance - Google Patents
Surface-coated cemented carbide cutting tool with excellent chipping resistanceInfo
- Publication number
- JP3353675B2 JP3353675B2 JP31810097A JP31810097A JP3353675B2 JP 3353675 B2 JP3353675 B2 JP 3353675B2 JP 31810097 A JP31810097 A JP 31810097A JP 31810097 A JP31810097 A JP 31810097A JP 3353675 B2 JP3353675 B2 JP 3353675B2
- Authority
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- Japan
- Prior art keywords
- layer
- thickness
- coated
- cutting
- cemented carbide
- 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.)
- Expired - Lifetime
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Description
【０００１】[0001]
【発明の属する技術分野】この発明は、従来表面被覆超
硬合金製切削工具の硬質被覆層を構成する酸化アルミニ
ウム（以下、Ａｌ2 Ｏ3 で示す）層の改良に係り、これ
を厚膜化してもその層厚が均一化すると共に、靭性低下
がなく、したがって例えば鋼や鋳鉄などの連続切削は勿
論のこと、特に断続切削に用いた場合にも切刃にチッピ
ング（微小欠け）などの発生なく、長期に亘ってすぐれ
た切削性能を発揮する表面被覆超硬合金製切削工具（以
下、被覆超硬工具と云う）に関するものである。BACKGROUND OF THE INVENTION The present invention, aluminum oxide which constitutes the hard coating layer of the conventional surface-coated cemented carbide cutting tool (hereinafter, Al 2 O indicated by 3) relates to an improvement of the layer, which thickened However, the layer thickness is uniform and there is no reduction in toughness. Therefore, not only continuous cutting of steel or cast iron, for example, but also chipping (small chipping) of the cutting edge particularly when used for intermittent cutting. In addition, the present invention relates to a surface-coated cemented carbide cutting tool that exhibits excellent cutting performance over a long period of time (hereinafter referred to as a coated cemented carbide tool).
【０００２】[0002]
【従来の技術】従来、一般に、例えば特開平６−３１５
０３号公報、特開平６−３１６７５８号公報、および特
開平７−２１６５４９号公報などに記載されるように、
炭化タングステン基超硬合金基体（以下、超硬基体とい
う）の表面に、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、ＴｉＣ
Ｏで示す）層、窒酸化物（以下、ＴｉＮＯで示す）層、
および炭窒酸化物（以下、ＴｉＣＮＯで示す）層からな
るＴｉ化合物層のうちの１層以上と、Ａｌ2 Ｏ3 層とで
構成され、前記Ｔｉ化合物層はいずれも粒状結晶組織を
有し、また前記ＴｉＣＮ層には縦長成長結晶組織をもつ
ものもあり、さらに前記Ａｌ2 Ｏ3 層はα型またはκ型
結晶組織をもつものである硬質被覆層を３〜２０μｍの
平均層厚で化学蒸着および／または物理蒸着してなる被
覆超硬工具が知られている。2. Description of the Related Art Conventionally, generally, for example, Japanese Patent Application Laid-Open No. 6-315
03, JP-A-6-316758, and JP-A-7-216549, etc.
A carbide of Ti (hereinafter, referred to as TiC) is formed on the surface of a tungsten carbide-based cemented carbide substrate (hereinafter, referred to as a cemented carbide substrate).
Layer, nitride (hereinafter also indicated by TiN) layer, carbonitride (hereinafter indicated by TiCN) layer, carbonate (hereinafter referred to as TiC)
O) layer, a nitride oxide (hereinafter referred to as TiNO) layer,
And at least one Ti compound layer composed of a carbonitride oxide (hereinafter, referred to as TiCNO) layer and an Al 2 O 3 layer, each of the Ti compound layers having a granular crystal structure, Some of the TiCN layers have a vertically-grown crystal structure, and the Al 2 O 3 layer has a hard coating layer having an α-type or κ-type crystal structure by chemical vapor deposition with an average layer thickness of 3 to 20 μm. A coated carbide tool formed by physical vapor deposition is known.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の切削加工
のＦＡ化はめざましく、かつ省力化に対する要求も強
く、これに伴い、被覆超硬工具には使用寿命のさらなる
延命化が求められ、これに対応する手段として、これを
構成する硬質被覆層のうち、特に耐酸化性と熱的安定性
にすぐれ、さらに高硬度を有するＡｌ2 Ｏ3 層の厚膜化
が広く検討されているが、前記Ａｌ2 Ｏ3 層は、これを
厚くすると、層厚が局部的に不均一になり、切刃の逃げ
面、すくい面、および前記逃げ面とすくい面の交わるエ
ッジ部の間には層厚に著しいバラツキが発生するように
なり、さらに厚膜化によるＡｌ2 Ｏ3層自体の靭性低下
も避けられず、この結果、例えば鋼や鋳鉄などの断続切
削に用いた場合に切刃にチッピングが発生し易く、これ
が原因で比較的短時間で使用寿命に至るのが現状であ
る。On the other hand, in recent years, the use of FA in cutting has been remarkable, and there has been a strong demand for labor saving. Accordingly, coated carbide tools have been required to have a longer service life. As means corresponding to the above, among the hard coating layers constituting the same, particularly, the oxidation resistance and thermal stability are excellent, and further thickening of an Al 2 O 3 layer having high hardness has been widely studied. When the Al 2 O 3 layer is thickened, the layer thickness becomes locally non-uniform, and the layer thickness is formed between the flank of the cutting edge, the rake face, and the edge portion where the flank and the rake face intersect. In addition, remarkable variation occurs, and the toughness of the Al 2 O 3 layer itself is inevitably reduced due to the thickening of the film. As a result, when used for interrupted cutting of steel or cast iron, for example, chipping occurs on the cutting edge. Easy to occur, which causes a relatively short time From reaching the service life it is at present.
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者等は、
上述のような観点から、被覆超硬工具の硬質被覆層を構
成するＡｌ2 Ｏ3 層に着目し、厚膜化した場合の層厚の
局部的バラツキの減少と靭性低下の抑制を図るべく研究
を行った結果、 （ａ） 化学蒸着法および／または物理蒸着法にて、 反応ガス組成（容量％で、以下同じ）−ＴｉＣｌ4 ：
０．４〜１０％、Ｃｏ2：０．４〜１０％、Ｎ2 ：５〜
６０％、Ｈ2 ：残り、 雰囲気温度：８００〜１１００℃、 雰囲気圧力：３０〜５００Ｔｏｒｒ、 の条件で蒸着を行うと、三酸化二チタン（以下、Ｔｉ2
Ｏ3 で示す）層が形成され、このＴｉ2 Ｏ3 層は、図１
に例示されるように、３４．５±１度の回折角（２θ）
に最高回折ピーク高さが現れるＸ線回折パターンを示
し、Ａｌ2 Ｏ3 層に対する密着性にすぐれると共に、自
身も良好な靭性をもつものであること。 （ｂ） したがって、基本的に、所定層厚のＡｌ2 Ｏ3
層を形成した後に、上記のＴｉ2 Ｏ3 層を所定層厚で形
成し、さらに再び所定層厚のＡｌ2 Ｏ3 層を形成する交
互積層構造層、すなわち所定層厚のＡｌ2 Ｏ3 層の２層
以上と、所定層厚のＴｉ2 Ｏ3 層の１層以上の交互積層
構造層においては、これを厚膜化しても、これを構成す
るＡｌ2 Ｏ3 層個々の層厚を相対的に薄くすることがで
きるので、その層厚に局部的バラツキが著しく少なくな
り、切刃の逃げ面、すくい面、および前記逃げ面とすく
い面の交わるエッジ部の層厚が相互に均一化するように
なり、加えてＡｌ2 Ｏ3 層自体を厚膜化した場合に発生
する靭性低下が著しく抑制されるようになること。 （ｃ） この結果硬質被覆層が、それぞれ所定層厚の上
記Ａｌ2 Ｏ3 層の２層以上および上記Ｔｉ2 Ｏ3 層の１
層以上の交互積層構造層と、所定層厚の上記Ｔｉ化合物
層のうちの１種または２種以上で構成された被覆超硬工
具は、前記Ａｌ 2 Ｏ3 層によって、硬質被覆層にすぐれ
た耐酸化性と熱的安定性、および高硬度が確保され、か
つ前記Ｔｉ2 Ｏ3 層によって、前記交互積層構造層に、
これを厚膜化しても良好な靭性が確保されることから、
例えば鋼や鋳鉄などの連続切削は勿論のこと、断続切削
に用いた場合にも切刃にチッピングなどの発生なく、長
期に亘ってすぐれた切削性能を発揮するようになるこ
と、以上（ａ）〜（ｃ）に示される研究結果を得たので
ある。Means for Solving the Problems Accordingly, the present inventors have
From the viewpoint as described above, the hard coating layer of the coated carbide tool is formed.
Al formedTwo OThree Focusing on the layer, the thickness of the layer
Study to reduce local variation and toughness
(A) Reaction gas composition (% by volume, the same applies hereinafter) -TiCl by chemical vapor deposition and / or physical vapor depositionFour :
0.4-10%, CoTwo: 0.4 to 10%, NTwo : 5
60%, HTwo : Atmosphere temperature: 800 to 1100 ° C., Atmospheric pressure: 30 to 500 Torr.Two
OThree Is formed, and this TiTwo OThree The layers are shown in FIG.
34.5 ± 1 degree diffraction angle (2θ)
X-ray diffraction pattern showing the highest diffraction peak height
And AlTwo OThree Excellent adhesion to the layer
The body must also have good toughness. (B) Therefore, basically, Al having a predetermined layer thicknessTwo OThree
After forming the layer, the TiTwo OThree Layers are formed with a predetermined thickness
And again with a predetermined layer thickness of AlTwo OThree Interchange forming layers
Alternating structure layers, that is, Al of a predetermined layer thicknessTwo OThree Two layers of layers
With the above, Ti of a predetermined layer thicknessTwo OThree Alternate stacking of one or more layers
In the structural layer, even if it is made thicker,
AlTwo OThree The thickness of each layer can be made relatively thin.
So that local variations in the layer thickness are significantly reduced.
Flank, rake face of the cutting edge, and flank
So that the layer thickness at the edges where
And in addition to AlTwo OThree Occurs when the layer itself is thickened
That the toughness decrease is significantly suppressed. (C) As a result, each of the hard coating layers is
Note AlTwo OThree Two or more layers and the TiTwo OThree Layer 1
And a Ti-compound having a predetermined layer thickness.
Coated cemented carbide composed of one or more layers
The tool is the Al TwoOThreeExcellent hard coating layer depending on the layer
Oxidation resistance and thermal stability, and high hardness
TiTwo OThree Depending on the layer,
Even if this is made thicker, good toughness is ensured,
For example, intermittent cutting as well as continuous cutting of steel, cast iron, etc.
No chipping etc. on the cutting edge even when used for
To achieve excellent cutting performance over time.
And obtained the research results shown in (a) to (c) above.
is there.
【０００５】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、超硬基体の表面に、ＴｉＣ層、Ｔ
ｉＮ層、ＴｉＣＮ層、ＴｉＣＯ層、ＴｉＮＯ層、および
ＴｉＣＮＯ層からなるＴｉ化合物層のうちの１層以上
と、交互積層構造層とで構成された硬質被覆層を３〜２
５μｍの平均層厚で形成してなる被覆超硬工具にして、
前記交互積層構造層を、０．５〜７μｍの平均層厚を有
するＡｌ2 Ｏ3 層の２層以上と、０．０５〜２μｍの平
均層厚を有し、かつＣｕｋα線を線源として用いたＸ線
回折で、３４．５±１度の回折角（２θ）に最高回折ピ
ーク高さが現れるＸ線回折パターンを示すＴｉ2 Ｏ3 層
の１層以上の交互積層構造層、で構成してなる、特に厚
膜化した場合の層厚の均一化および靭性低下の抑制をは
かり、これによって切刃の耐チッピング性を向上せしめ
た被覆超硬工具に特徴を有するものである。The present invention has been made on the basis of the above research results, and a TiC layer and a T
A hard coating layer composed of at least one layer of a Ti compound layer including an iN layer, a TiCN layer, a TiCO layer, a TiNO layer, and a TiCNO layer, and an alternately laminated structure layer is 3 to 2
A coated carbide tool formed with an average layer thickness of 5 μm,
The alternate layered structure layer has two or more Al 2 O 3 layers having an average layer thickness of 0.5 to 7 μm and an average layer thickness of 0.05 to 2 μm, and uses a Cukα ray as a radiation source. And at least one alternate layered structure layer of Ti 2 O 3 layers showing an X-ray diffraction pattern in which the highest diffraction peak height appears at a diffraction angle (2θ) of 34.5 ± 1 degree. In particular, the present invention has a feature in a coated carbide tool in which the thickness of the coating is made uniform, and the reduction in toughness is suppressed, and thereby the chipping resistance of the cutting edge is improved.
【０００６】なお、この発明の被覆超硬工具の硬質被覆
層を構成する交互積層構造層において、Ａｌ2 Ｏ3 層の
個々の平均層厚を０．５〜７μｍとしたのは、その層厚
が０．５μｍ未満では、これを多重積層しても、これの
もつすぐれた耐酸化性と熱的安定性、および高硬度を硬
質被覆層に具備せしめることができず、一方その層厚が
７μｍを越えると、硬質被覆層の層厚の均一化が損なわ
れ、かつ硬質被覆層の靭性が低下するようになるという
理由にもとづくものであり、また同じくＴｉ2Ｏ3 層の
個々の平均層厚を０．０５〜２μｍとしたのは、その層
厚が０．０５μｍ未満では、Ｔｉ2 Ｏ3 層のもつ上記の
特性、すなわちＡｌ2 Ｏ3 層に対するすぐれた密着性お
よび交互積層構造層を厚膜化した場合の靭性を確保する
ことができず、一方その層厚が２μｍを越えると、硬質
被覆層の耐摩耗性が急激に低下するようになるという理
由によるものである。さらに、硬質被覆層の平均層厚を
３〜２５μｍとしたのは、その層厚が３μｍ未満では所
望のすぐれた耐摩耗性を確保することができず、一方そ
の層厚が２５μｍを越えると、切刃の耐チッピング性が
低下するようになるという理由からである。The average thickness of each of the Al 2 O 3 layers in the alternating layered structure layer constituting the hard coating layer of the coated carbide tool according to the present invention is set to 0.5 to 7 μm. Is less than 0.5 μm, it is not possible to provide the hard coating layer with its excellent oxidation resistance, thermal stability, and high hardness even when multiple layers are laminated, while the layer thickness is 7 μm. Is exceeded, the uniformity of the thickness of the hard coating layer is impaired, and the toughness of the hard coating layer is reduced, and the average thickness of the individual Ti 2 O 3 layers is also reduced. Is set to 0.05 to 2 μm because, when the layer thickness is less than 0.05 μm, the above-mentioned properties of the Ti 2 O 3 layer, that is, excellent adhesion to the Al 2 O 3 layer and thickness The toughness of the film cannot be secured, while If the thickness exceeds 2 [mu] m, it is due because the wear resistance of the hard coating layer will be lowered rapidly. Furthermore, the reason why the average layer thickness of the hard coating layer is set to 3 to 25 μm is that if the layer thickness is less than 3 μm, it is not possible to secure desired excellent wear resistance, while if the layer thickness exceeds 25 μm, This is because the chipping resistance of the cutting edge is reduced.
【０００７】[0007]
【発明の実施の形態】つぎに、この発明の被覆超硬工具
を実施例により具体的に説明する。原料粉末として、平
均粒径：２．８μｍを有する中粒ＷＣ粉末、同４．９μ
ｍの粗粒ＷＣ粉末、同１．５μｍの（Ｔｉ，Ｗ）Ｃ（重
量比で、以下同じ、ＴｉＣ／ＷＣ＝３０／７０）粉末、
同１．２μｍの（Ｔｉ，Ｗ）ＣＮ（ＴｉＣ／ＴｉＮ／Ｗ
Ｃ＝２４／２０／５６）粉末、同１．２μｍの（Ｔａ，
Ｎｂ）Ｃ（ＴａＣ／ＮｂＣ＝９０／１０）粉末、および
同１．１μｍの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、ボールミルで７２時間
湿式混合し、乾燥した後、ＩＳＯ・ＣＮＭＧ１２０４０
８（超硬基体Ａ〜Ｄ用）および同ＳＥＥＮ４２ＡＦＴＮ
１（超硬基体Ｅ用）に定める形状の圧粉体にプレス成形
し、この圧粉体を同じく表１に示される条件で真空焼結
することにより超硬基体Ａ〜Ｅをそれぞれ製造した。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the coated carbide tool of the present invention will be specifically described with reference to examples. Medium-sized WC powder having an average particle diameter of 2.8 μm, 4.9 μm as the raw material powder
m of coarse WC powder, 1.5 μm of (Ti, W) C (the same in weight ratio, hereinafter, TiC / WC = 30/70) powder,
1.2 μm (Ti, W) CN (TiC / TiN / W
C = 24/20/56) powder, 1.2 μm (Ta,
Nb) C (TaC / NbC = 90/10) powder and Co powder of 1.1 μm were prepared, and these raw material powders were blended in the composition shown in Table 1, wet-mixed in a ball mill for 72 hours, and dried. After that, ISO ・ CNMG12040
8 (for carbide substrates A to D) and SEEN42AFTN
Press molded into a green compact having the shape defined in No. 1 (for the super hard substrate E), and the green compact was vacuum-sintered under the conditions shown in Table 1 to produce super hard substrates A to E, respectively.
【０００８】さらに、上記超硬基体Ｂに対して、１００
ＴｏｒｒのＣＨ4 ガス雰囲気中、温度：１４００℃に１
時間保持後、徐冷の滲炭処理を施し、処理後、超硬基体
表面に付着するカーボンとＣｏを酸およびバレル研磨で
除去することにより、表面から１１μｍの位置で最大Ｃ
ｏ含有量：１５．９重量％、深さ：４２μｍのＣｏ富化
帯域を基体表面部に形成した。また、上記超硬基体Ａお
よびＤには、焼結したままで、表面部に表面から１７μ
ｍの位置で最大Ｃｏ含有量：９．１重量％、深さ：２３
μｍのＣｏ富化帯域が形成されており、残りの超硬基体
ＣおよびＥには、前記Ｃｏ富化帯域の形成がなく、全体
的に均質な組織をもつものであった。なお、表１には、
上記超硬基体Ａ〜Ｅの内部硬さ（ロックウエル硬さＡス
ケール）をそれぞれ示した。[0008] Further, 100
In a Torr CH 4 gas atmosphere, temperature: 1400 ° C
After holding for a while, a slow cooling carburizing treatment is performed, and after the treatment, carbon and Co adhering to the surface of the super-hard substrate are removed by acid and barrel polishing to obtain a maximum carbon at a position of 11 μm from the surface.
A Co-enriched zone having an o content of 15.9% by weight and a depth of 42 μm was formed on the surface of the substrate. In addition, the cemented carbide substrates A and D were kept sintered and 17 μm from the surface.
m, maximum Co content: 9.1% by weight, depth: 23
A Co-enriched zone of μm was formed, and the remaining cemented carbide substrates C and E did not have the Co-enriched zone and had an overall homogeneous structure. In Table 1,
The internal hardness (Rockwell hardness A scale) of each of the carbide substrates A to E is shown.
【０００９】ついで、これらの超硬基体Ａ〜Ｅの表面
に、ホーニングを施した状態で、通常の化学蒸着装置を
用い、表２（表中の縦長成長結晶組織を有するＴｉＣＮ
層は特開平６−８０１０号公報に記載されるＴｉＣＮ層
に相当するものである）に示される条件にて、表３、４
に示される組成および目標層厚（切刃の逃げ面）の硬質
被覆層を形成することにより本発明被覆超硬工具１〜１
０、および硬質被覆層がＴｉ化合物層とＡｌ2 Ｏ3 層で
構成され、Ｔｉ2 Ｏ3 層の形成がない従来被覆超硬工具
１〜１０をそれぞれ製造した。なお、図１は本発明被覆
超硬工具２のＴｉ2 Ｏ3 層形成直後のＸ線回折パターン
を示すものである。Then, the surface of each of the hard substrates A to E was honed, and the surface of each of the hard substrates A to E was subjected to Table 2 (TiCN having a vertically-grown crystal structure shown in the table) using an ordinary chemical vapor deposition apparatus.
The layers correspond to the TiCN layers described in JP-A-6-8010), and the conditions shown in Tables 3 and 4 were used.
By forming a hard coating layer having the composition and target layer thickness (flank of the cutting edge) shown in FIG.
No. 0, and the conventional coated carbide tools 1 to 10 in which the hard coating layer was composed of the Ti compound layer and the Al 2 O 3 layer, and the formation of the Ti 2 O 3 layer was not produced. FIG. 1 shows an X-ray diffraction pattern of the coated carbide tool 2 of the present invention immediately after the Ti 2 O 3 layer is formed.
【００１０】つぎに、上記本発明被覆超硬工具１、２お
よび従来被覆超硬工具１、２について、 被削材：ＪＩＳ・ＦＣＤ４５０の角材、 切削速度：２５０ｍ／ｍｉｎ．、 切込み：２ｍｍ、 送り：０．２５ｍｍ／ｒｅｖ．、 切削時間：５分、 の条件でダクタイル鋳鉄の乾式断続切削試験を行い、切
刃の逃げ面摩耗幅を測定した。Next, regarding the above-mentioned coated carbide tools 1 and 2 of the present invention and conventional coated carbide tools 1 and 2, a work material: a square material of JIS FCD450, a cutting speed: 250 m / min. , Depth of cut: 2 mm, feed: 0.25 mm / rev. A dry intermittent cutting test was performed on ductile cast iron under the following conditions: cutting time: 5 minutes, and the flank wear width of the cutting edge was measured.
【００１１】上記本発明被覆超硬工具３、４および従来
被覆超硬工具３、４については、 被削材：ＪＩＳ・ＳＣＭ４１５の角材、 切削速度：２５０ｍ／ｍｉｎ．、 切込み：２ｍｍ．、 送り：０．２５ｍｍ／ｒｅｖ．、 切削時間：５分、 の条件で合金鋼の乾式断続切削試験を行い、切刃の逃げ
面摩耗幅を測定した。The coated carbide tools 3 and 4 of the present invention and the conventional coated carbide tools 3 and 4 are as follows: work material: square material of JIS SCM415, cutting speed: 250 m / min. , Depth of cut: 2 mm. Feed: 0.25 mm / rev. , Cutting time: 5 minutes, a dry intermittent cutting test of the alloy steel was performed, and the flank wear width of the cutting edge was measured.
【００１２】上記本発明被覆超硬工具５、６および従来
被覆超硬工具５、６については、 被削材：ＪＩＳ・Ｓ４５Ｃの角材、 切削速度：２５０ｍ／ｍｉｎ．、 切込み：２ｍｍ．、 送り：０．２５ｍｍ／ｒｅｖ．、 切削時間：５分、 の条件で炭素鋼の乾式断続切削試験を行い、切刃の逃げ
面摩耗幅を測定した。The coated carbide tools 5 and 6 according to the present invention and the conventional coated carbide tools 5 and 6 are as follows: Work material: square material of JIS S45C; Cutting speed: 250 m / min. , Depth of cut: 2 mm. Feed: 0.25 mm / rev. A dry intermittent cutting test of carbon steel was performed under the following conditions: cutting time: 5 minutes, and the flank wear width of the cutting edge was measured.
【００１３】上記本発明被覆超硬工具７、８および従来
被覆超硬工具７、８については、 被削材：ＪＩＳ・ＦＣ２００の角材、 切削速度：２５０ｍ／ｍｉｎ．、 切込み：２ｍｍ．、 送り：０．２５ｍｍ／ｒｅｖ．、 切削時間：５分、 の条件で鋳鉄の乾式断続切削試験を行い、切刃の逃げ面
摩耗幅を測定した。The coated carbide tools 7 and 8 of the present invention and the conventional coated carbide tools 7 and 8 are as follows: Work material: square material of JIS FC200, Cutting speed: 250 m / min. , Depth of cut: 2 mm. Feed: 0.25 mm / rev. A dry intermittent cutting test of cast iron was performed under the following conditions: cutting time: 5 minutes, and the flank wear width of the cutting edge was measured.
【００１４】同じく本発明被覆超硬工具９、１０および
従来被覆超硬工具９、１０については、 被削材：幅１００ｍｍ×長さ５００ｍｍの寸法をもった
ＪＩＳ・ＳＣＭ４４０の角材、 使用条件：直径１２５ｍｍのカッターに単刃取り付け、 回転数：６４０ｒ．ｐ．ｍ．、 切削速度：２５０ｍ／ｍｉｎ．、 切込み：２ｍｍ．、 送り：０．２ｍｍ／刃、 切削時間：２パス（１パスの切削時間：４．３分）、 の条件で合金鋼の乾式フライス切削（断続切削）試験を
行い、切刃の逃げ面摩耗幅を測定した。これらの測定結
果を表５に示した。Similarly, for the coated carbide tools 9 and 10 of the present invention and the conventional coated carbide tools 9 and 10, a work material: a square material of JIS SCM440 having a size of 100 mm in width × 500 mm in length; A single blade is attached to a 125 mm cutter, rotation speed: 640 r. p. m. Cutting speed: 250 m / min. , Depth of cut: 2 mm. , Feed: 0.2mm / tooth, Cutting time: 2 passes (1 pass cutting time: 4.3 minutes), Dry milling (intermittent cutting) test of alloy steel under the following conditions: flank wear of cutting edge The width was measured. Table 5 shows the results of these measurements.
【００１５】[0015]
【表１】 [Table 1]
【００１６】[0016]
【表２】 [Table 2]
【００１７】[0017]
【表３】 [Table 3]
【００１８】[0018]
【表４】 [Table 4]
【００１９】[0019]
【表５】 [Table 5]
【００２０】[0020]
【発明の効果】表３〜５に示される結果から、硬質被覆
層が、Ａｌ2 Ｏ3 層およびＴｉ2 Ｏ3層の交互積層構造
層とＴｉ化合物層からなる本発明被覆超硬工具１〜１０
は、いずれも前記Ｔｉ2 Ｏ3 層の作用で前記Ａｌ2 Ｏ3
層を総合的に厚膜化しても硬質被覆層の靭性低下が著し
く抑制され、かつ層厚の局部的バラツキがきわめて少な
く、切刃の逃げ面、すくい面、および逃げ面とすくい面
の交わるエッジ部の層厚が均一化しているのに対して、
硬質被覆層がＡｌ2 Ｏ3 層とＴｉ化合物層からなる従来
被覆超硬工具１〜１０においては、前記Ａｌ2 Ｏ3 層を
厚膜化した場合、硬質被覆層の靭性低下が避けられず、
かつ層厚のバラツキも著しく、この結果として本発明被
覆超硬工具１〜１０は、前記従来被覆超硬工具１〜１０
に比して、鋼および鋳鉄の断続切削で一段とすぐれた耐
チッピング性を示すことが明らかである。上述のよう
に、この発明の被覆超硬工具は、これの硬質被覆層を構
成するＡｌ 2 Ｏ3 層はＴｉ2 Ｏ3 層との交互積層による
厚膜化なので、硬質被覆層の靭性低下がなく、さらに層
厚の局部的バラツキもきわめて少ないことから、例えば
鋼や鋳鉄などの連続切削は勿論のこと、特に断続切削に
おいて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で、切削加工のＦＡ化およ
び省力化に満足に対応することができるものである。According to the results shown in Tables 3 to 5, the hard coating
The layer is AlTwoOThreeLayer and TiTwo OThreeAlternating layer structure
Tool coated with the present invention comprising a titanium layer and a Ti compound layer
Are all the TiTwo OThree The action of the layerTwoOThree
Even if the thickness of the layer is increased, the toughness of the hard coating layer decreases significantly.
And local variations in layer thickness are extremely small.
Rake face, rake face, rake face and rake face
Where the layer thickness at the intersection where
Hard coating layer is AlTwoOThreeLayer consisting of a layer and a Ti compound layer
In the coated carbide tools 1 to 10, the above AlTwoOThreeLayers
When the film thickness is increased, the toughness of the hard coating layer is inevitably reduced,
In addition, the thickness of the layer varies significantly, and as a result,
The coated carbide tools 1 to 10 are the conventional coated carbide tools 1 to 10
More excellent resistance to interrupted cutting of steel and cast iron
It is clear that it shows chipping properties. As mentioned above
In addition, the coated cemented carbide tool of the present invention comprises this hard coating layer.
Al formed TwoOThreeThe layer is TiTwo OThree By alternate lamination with layers
Because the film is thicker, there is no decrease in toughness of the hard coating layer.
Since the local variation of the thickness is extremely small, for example,
For continuous cutting of steel and cast iron, of course, especially for interrupted cutting
Excellent chipping resistance for a long time
Because of its outstanding cutting performance, it is
It can respond satisfactorily to labor and labor saving.
【図１】本発明被覆超硬工具２のＴｉ2 Ｏ3 層形成直後
のＸ線回折パターンを示す図である。FIG. 1 is a view showing an X-ray diffraction pattern immediately after forming a Ti 2 O 3 layer of a coated carbide tool 2 of the present invention.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ Ｃ２３Ｃ 16/40 Ｃ２３Ｃ 16/40 (72)発明者 柳田 一也 埼玉県大宮市北袋町１−297 三菱マテ リアル株式会社 総合研究所内 (56)参考文献 特開 平11−92936（ＪＰ，Ａ) 特開 平11−77405（ＪＰ，Ａ) 特開 平10−310877（ＪＰ，Ａ) 特開 昭59−219477（ＪＰ，Ａ) 特許2529190（ＪＰ，Ｂ２) 特公 平５−49750（ＪＰ，Ｂ２) 特公 昭62−6748（ＪＰ，Ｂ１) 特公 昭58−24502（ＪＰ，Ｂ１) (58)調査した分野(Int.Cl.7，ＤＢ名) B23B 27/14 C23C 14/08 C23C 16/30 C23C 16/40 ──────────────────────────────────────────────────続 き Continued on front page (51) Int.Cl. 7 Identification code FI C23C 16/40 C23C 16/40 (72) Inventor Kazuya Yanagita 1-297 Kitabukurocho, Omiya City, Saitama Prefecture Mitsubishi Materials Corporation In-house (56) References JP-A-11-92936 (JP, A) JP-A-11-77405 (JP, A) JP-A-10-310877 (JP, A) JP-A-59-219477 (JP, A) Patent 2529190 (JP, B2) JP-B 5-49750 (JP, B2) JP-B 62-6748 (JP, B1) JP-B 58-24502 (JP, B1) (58) Fields investigated (Int. . 7, DB name) B23B 27/14 C23C 14/08 C23C 16/30 C23C 16/40
Claims (1)
に、Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物
層、窒酸化物層、および炭窒酸化物層からなるＴｉ化合
物層のうちの１層以上と、交互積層構造層とで構成され
た硬質被覆層を３〜２５μｍの平均層厚で化学蒸着およ
び／または物理蒸着してなる表面被覆超硬合金製切削工
具にして、前記交互積層構造層を、 ０．５〜７μｍの平均層厚を有する酸化アルミニウム層
の２層以上と、 ０．０５〜２μｍの平均層厚を有し、かつＣｕｋα線を
線源として用いたＸ線回折で、３４．５±１度の回折角
（２θ）に最高回折ピーク高さが現れるＸ線回折パター
ンを示す三酸化二チタン層の１層以上の交互積層構造層
で構成したこと、を特徴とする耐チッピング性のすぐれ
た表面被覆超硬合金製切削工具。1. A Ti compound layer comprising a carbide layer, a nitride layer, a carbonitride layer, a carbonate layer, a carbonitride layer, and a carbonitride layer on a surface of a tungsten carbide-based cemented carbide substrate. A hard-coated layer composed of at least one of the above and an alternately laminated structure layer is a surface-coated hard metal cutting tool formed by chemical vapor deposition and / or physical vapor deposition with an average layer thickness of 3 to 25 μm. The alternate layered structure layer is composed of two or more aluminum oxide layers having an average layer thickness of 0.5 to 7 μm, X having an average layer thickness of 0.05 to 2 μm, and using Cuka radiation as a radiation source. A diffraction angle (2θ) of 34.5 ± 1 degrees in X-ray diffraction, wherein at least one alternately laminated layer of dititanium trioxide showing an X-ray diffraction pattern showing a maximum diffraction peak height. Surface-coated cemented carbide cutting with excellent chipping resistance Ingredients.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31810097A JP3353675B2 (en) | 1997-11-19 | 1997-11-19 | Surface-coated cemented carbide cutting tool with excellent chipping resistance |
| DE69802035T DE69802035T2 (en) | 1997-05-12 | 1998-05-12 | Coated cutting tool |
| EP98108570A EP0878563B1 (en) | 1997-05-12 | 1998-05-12 | Coated cutting tool member |
| US09/075,923 US6071601A (en) | 1997-05-12 | 1998-05-12 | Coated cutting tool member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP31810097A JP3353675B2 (en) | 1997-11-19 | 1997-11-19 | Surface-coated cemented carbide cutting tool with excellent chipping resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11152570A JPH11152570A (en) | 1999-06-08 |
| JP3353675B2 true JP3353675B2 (en) | 2002-12-03 |
Family
ID=18095497
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP31810097A Expired - Lifetime JP3353675B2 (en) | 1997-05-12 | 1997-11-19 | Surface-coated cemented carbide cutting tool with excellent chipping resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3353675B2 (en) |
Families Citing this family (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE519339C2 (en) * | 2000-11-22 | 2003-02-18 | Sandvik Ab | Cutting tools coated with alumina and ways of manufacturing the same |
| SE528891C2 (en) * | 2005-03-23 | 2007-03-06 | Sandvik Intellectual Property | Cut coated with a multi-layer of metal oxide |
| SE528929C2 (en) | 2005-04-18 | 2007-03-20 | Sandvik Intellectual Property | Cut coated with a layer system and method of making this |
| JP6330359B2 (en) * | 2014-02-14 | 2018-05-30 | 新日鐵住金株式会社 | Carbide tool |
-
1997
- 1997-11-19 JP JP31810097A patent/JP3353675B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH11152570A (en) | 1999-06-08 |
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