JP2001322006A - Surface coated cemented carbide cutting tool with excellent wear resistance - Google Patents
Surface coated cemented carbide cutting tool with excellent wear resistanceInfo
- Publication number
- JP2001322006A JP2001322006A JP2000140658A JP2000140658A JP2001322006A JP 2001322006 A JP2001322006 A JP 2001322006A JP 2000140658 A JP2000140658 A JP 2000140658A JP 2000140658 A JP2000140658 A JP 2000140658A JP 2001322006 A JP2001322006 A JP 2001322006A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- coating layer
- cemented carbide
- composite
- cutting
- 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.)
- Pending
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Landscapes
- Powder Metallurgy (AREA)
- Physical Vapour Deposition (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、すぐれた耐摩耗
性を有し、したがって例えば鋼の連続切削や断続切削で
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、被覆超硬切削工具と云う）に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cutting tool made of a surface-coated cemented carbide which has excellent wear resistance and therefore exhibits excellent cutting performance over a long period of time, for example, in continuous cutting and interrupted cutting of steel. Hereinafter, referred to as a coated carbide cutting tool).
【０００２】[0002]
【従来の技術】従来、一般に、例えば図１に概略説明図
で示される物理蒸着装置の１種であるアークイオンプレ
ーティング装置を用い、ヒータで装置内を例えば７００
℃の温度に加熱した状態で、アノード電極と所定組成を
有するＴｉ−Ａｌ合金がセットされたカソード電極（蒸
発源）との間にアーク放電を発生させ、同時に装置内に
反応ガスとして窒素ガス、または窒素ガスとメタンガス
を導入し、一方炭化タングステン（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）基サーメットからなる工具基体（以下、これらを総
称して超硬工具基体と云う）には、例えば−１２０Ｖの
バイアス電圧を印加した条件で、前記超硬工具基体の表
面に、例えば特開昭６２−５６５６５号公報に記載され
るように、ＴｉとＡｌの複合窒化物［以下、（Ｔｉ，Ａ
ｌ）Ｎで示す］層および複合炭窒化物［以下、（Ｔｉ，
Ａｌ）ＣＮで示す］層のうちの１種の単層または２種の
複層からなる強靭性被覆層を０．５〜１５μｍの平均層
厚で物理蒸着することにより製造された被覆超硬切削工
具が知られている。2. Description of the Related Art Conventionally, for example, an arc ion plating apparatus, which is a kind of physical vapor deposition apparatus schematically shown in FIG.
In the state heated to a temperature of ° C., an arc discharge is generated between the anode electrode and a cathode electrode (evaporation source) on which a Ti-Al alloy having a predetermined composition is set, and at the same time, nitrogen gas as a reaction gas is introduced into the apparatus. Alternatively, nitrogen gas and methane gas are introduced, while tungsten carbide (hereinafter referred to as WC)
A tool base made of a base cemented carbide or a titanium cermet (hereinafter, referred to as TiCN) base cermet (hereinafter, collectively referred to as a cemented carbide tool base) is applied under a condition that a bias voltage of -120 V is applied, for example. As described in, for example, JP-A-62-56565, a composite nitride of Ti and Al [hereinafter, (Ti, A
1) N]] layer and composite carbonitride [hereinafter, (Ti,
Al) [CN]], a coated hard cut produced by physical vapor deposition of a tough coating layer consisting of one single layer or two or more layers of the layers with an average layer thickness of 0.5 to 15 μm. Tools are 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化および高速化はめざましく、かつ切削加工の省
力化および省エネ化に対する要求もつよく、これに伴
い、切削工具には使用寿命の延命化が強く望まれている
が、上記の従来被覆超硬切削工具の場合、これを構成す
る（Ｔｉ，Ａｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層から
なる強靭性被覆層はすぐれた強度および靭性を有し、良
好な耐チッピング性（工具切刃に微小欠けが発生しにく
い性質）を示すものの、耐摩耗性が十分でないために、
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, FA and speed of cutting have been remarkable, and there is also a demand for labor saving and energy saving of cutting. As a result, the life of cutting tools has been extended. However, in the case of the above-mentioned conventional coated carbide cutting tool, the tough coating layer composed of the (Ti, Al) N layer and the (Ti, Al) CN layer has excellent strength and strength. Although it has toughness and shows good chipping resistance (the property that micro chipping does not easily occur on the tool cutting edge), it has insufficient wear resistance,
At present, the service life is reached in a relatively short time.
【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、上記の従来被覆超硬切削工具の
耐摩耗性向上を図るべく、特にこれを構成する硬質被覆
層に着目し、研究を行なった結果、 （ａ）物理蒸着法により形成された通常のＡｌ2 Ｏ3被
覆層は、耐熱性にすぐれ、かつ高硬度を有することか
ら、耐摩耗性向上を図る上で望ましいものであるが、前
記Ａｌ2 Ｏ3被覆層は上記の従来被覆超硬切削工具を構
成する（Ｔｉ，Ａｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層
との密着性に劣るものであることから、前記従来被覆超
硬切削工具の表面に前記Ａｌ2 Ｏ3被覆層を形成してな
る被覆超硬切削工具においては、特に工具切刃に高い負
荷のかかる断続切削を高切込みや高送りなどの重切削条
件で行った場合に前記Ａｌ2 Ｏ3被覆層に剥離が発生し
易く、実用に供することができないこと。Means for Solving the Problems Accordingly, the present inventors have
In view of the above, in order to improve the wear resistance of the conventional coated carbide cutting tool, a study was conducted by paying particular attention to the hard coating layer constituting the cutting tool. typical Al 2 O 3 coating layer is, excellent heat resistance, and because it has a high hardness, but is desirable in achieving the wear resistance improvement, the Al 2 O 3 coating layer is conventional the Since the adhesiveness between the (Ti, Al) N layer and the (Ti, Al) CN layer constituting the coated carbide cutting tool is poor, the surface of the conventional coated carbide cutting tool is coated with the Al 2 O 3. In a coated carbide cutting tool having a coating layer formed thereon, particularly when performing intermittent cutting with a high load on the tool cutting edge under heavy cutting conditions such as high cutting or high feed, the Al 2 O 3 coating layer Peeling easily occurs and cannot be put to practical use.
【０００５】（ｂ）上記の従来被覆超硬切削工具を構成
する（Ｔｉ，Ａｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層の
表面に、まず、ＴｉとＡｌの複合炭酸化物［以下、（Ｔ
ｉ，Ａｌ）ＣＯで示す］層および／またはＴｉとＡｌの
複合炭窒酸化物［以下、（Ｔｉ，Ａｌ）ＣＮＯで示す］
層を物理蒸着し、この上に、Ａｌよりイオン半径の大き
いＴａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒ、すなわちイオ
ン半径が０．５７オングストロームのＡｌに対して、そ
れぞれイオン半径が０．６８オングストロームのＴａ、
同０．６９オングストロームのＮｂ、および同０．６５
オングストロームのＶ、同０．６４オングストロームの
Ｃｒ、同０．６８オングストロームのＭｏおよび同０．
６８オングストロームのＷうちの１種または２種以上
を、Ａｌ2 Ｏ3 の結晶構造におけるＡｌ原子の一部をＡ
ｌとの合量に占める割合で５〜２０原子％、望ましくは
７〜１５原子％の割合で置換した形で固溶含有してなる
Ａｌ2 Ｏ3 主体層を物理蒸着させると、 この結果のＡ
ｌ 2 Ｏ3のもつ結晶構造を保持したままのＡｌ2 Ｏ3 主
体層は、大きなイオン半径差による格子内歪みの著しい
増大によって、通常の物理蒸着形成したＡｌ2 Ｏ3被覆
層が層厚にも影響されるが０．２〜０．８ＧＰａの圧縮
残留応力をもつのに対して、１〜２ＧＰａの圧縮残留応
力をもつようになり、このように圧縮残留応力の高いＡ
ｌ2Ｏ3主体層は上記（Ｔｉ，Ａｌ）ＣＯ層および（Ｔ
ｉ，Ａｌ）ＣＮＯ層に著しく強固に密着し、かつＡｌ2
Ｏ3の具備する特性をそのまま保持し、一方前記（Ｔ
ｉ，Ａｌ）ＣＯ層および（Ｔｉ，Ａｌ）ＣＮＯ層は前記
（Ｔｉ，Ａｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層に対す
る密着性にすぐれたものであるから、前記（Ｔｉ，Ａ
ｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層の表面に、さらに
前記（Ｔｉ，Ａｌ）ＣＯ層および（Ｔｉ，Ａｌ）ＣＮＯ
層を介して前記Ａｌ2 Ｏ3 主体層を物理蒸着してなる被
覆超硬切削工具は、例えば鋼の断続切削を、特に工具切
刃に高い負荷のかかる高切込みや高送りなどの重切削条
件で行っても前記Ａｌ2Ｏ3 主体層に剥離の発生なく、
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。以上（ａ）および（ｂ）に示される研究結果を得た
のである。(B) Constituting the above-mentioned conventional coated carbide cutting tool
(Ti, Al) N layer and (Ti, Al) CN layer
First, a composite carbonate of Ti and Al [hereinafter, (T
i, Al) CO] layer and / or Ti and Al
Complex carbonitrides [Hereinafter indicated by (Ti, Al) CNO]
Physically vapor-deposited a layer, having a larger ionic radius than Al
Ta, V, Nb, W, Mo and Cr,
For Al with a radius of 0.57 angstroms,
Ta, each having an ion radius of 0.68 angstroms,
0.69 angstroms of Nb and 0.65 of Nb
Angstrom V, 0.64 Angstrom
Cr, Mo of 0.68 angstroms and Cr of 0.08 angstroms.
One or more of W of 68 Å
With AlTwoOThreeSome of the Al atoms in the crystal structure of
5 to 20 atomic% in the total amount with l, desirably
Solid solution contained in a form substituted at a rate of 7 to 15 atomic%
AlTwoOThreeWhen the main layer is physically vapor-deposited,
l TwoOThreeAl while retaining the crystal structure ofTwoOThreemain
The body layer has significant intra-lattice strain due to large ion radius difference.
By increasing the normal physical vapor deposited AlTwoOThreeCoating
Layer is affected by layer thickness, but compression of 0.2-0.8 GPa
While having residual stress, compressive residual stress of 1-2 GPa
A with high compressive residual stress
lTwoOThreeThe main layer is composed of the (Ti, Al) CO layer and the (T
i, Al) adheres very strongly to the CNO layer andTwo
OThreeWhile maintaining the characteristics of (T)
The (i, Al) CO layer and the (Ti, Al) CNO layer are as described above.
(Ti, Al) N layer and (Ti, Al) CN layer
(Ti, A)
1) On the surface of the N layer and the (Ti, Al) CN layer,
The (Ti, Al) CO layer and the (Ti, Al) CNO
Through the layerTwoOThreeThe substrate formed by physical vapor deposition of the main layer
Coated carbide cutting tools are used, for example, for interrupted cutting of steel, especially tool cutting.
Heavy cutting strips such as high depth of cut and high feed with high load on the blade
AlTwoOThreeNo peeling of the main layer,
It will exhibit excellent wear resistance over a long period of time
When. The research results shown in (a) and (b) above were obtained.
It is.
【０００６】この発明は、上記の研究結果にもとづいて
なされたものであって、超硬工具基体の表面に、（Ｔ
ｉ，Ａｌ）Ｎ層および（Ｔｉ，Ａｌ）ＣＮ層のうちの１
種の単層または２種の複層からなる強靭性被覆層を０．
５〜１５μｍの平均層厚で物理蒸着してなる被覆超硬切
削工具において、上記強靭性被覆層の表面に、さらに
０．１〜１０μｍの平均層厚を有する（Ｔｉ，Ａｌ）Ｃ
Ｏ層および（Ｔｉ，Ａｌ）ＣＮＯ層のうちの１種の単層
または２種の複層からなる密着性中間被覆層を介して、
Ａｌ2 Ｏ3のもつ結晶構造を保持したままで、Ａｌの一
部をＡｌとの合量に占める割合で５〜２０原子％のＴ
ａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒのうちの１種または
２種以上で置換固溶してなるＡｌ2 Ｏ3主体層からなる
耐摩耗性被覆層を５〜１５μｍの平均層厚で物理蒸着し
てなる、耐摩耗性のすぐれた被覆超硬切削工具に特徴を
有するものである。The present invention has been made based on the results of the above-mentioned research, and has the following features: (T)
one of the (i, Al) N layer and the (Ti, Al) CN layer
A tough coating layer consisting of one kind of single layer or two kinds of multiple layers is used.
In a coated carbide cutting tool formed by physical vapor deposition with an average layer thickness of 5 to 15 μm, (Ti, Al) C further has an average layer thickness of 0.1 to 10 μm on the surface of the tough coating layer.
Through an adhesive intermediate coating layer composed of one type of single layer or two types of multiple layers of the O layer and the (Ti, Al) CNO layer,
While maintaining the crystal structure of Al 2 O 3 , T is 5 to 20 atomic% as a proportion of the total amount of Al with Al.
a, V, Nb, W, one or abrasion resistant coating layer comprising a formed by replacing solid solution Al 2 O 3 based layer in two or more of Mo and Cr in an average layer thickness of 5~15μm physical The present invention is characterized by a coated carbide cutting tool having excellent wear resistance formed by vapor deposition.
【０００７】なお、この発明の被覆超硬切削工具におい
て、これを構成する強靭性被覆層、密着性中間被覆層、
および耐摩耗性被覆層の平均層厚を上記の通りに限定し
た理由を説明する。 （ａ）強靭性被覆層 その平均層厚が０．５μｍ未満では所望のすぐれた強靭
性を確保することができず、この結果切刃に欠けやチッ
ピング（微小欠け）が発生し易くなり、一方その層厚が
１５μｍを越えると切削時に発生する高熱によって熱塑
性変形を起し、切刃に偏摩耗が発生し、これが原因で摩
耗進行が急激に促進されるようになることから、その平
均層厚を０．５〜１５μｍと定めた。 （ｂ）密着性中間被覆層 その平均層厚が０．１μｍ未満では、上記の強靭性被覆
層と耐摩耗性被覆層との間に強固な密着性を確保するこ
とができず、一方その平均層厚が１０μｍを越えると、
物理蒸着被覆層全体の脆化を促進し、切刃に欠けやチッ
ピングが発生し易くなることから、その平均層厚を０．
１〜１０μｍと定めた。 （ｃ）耐摩耗性被覆層 その平均層厚が０．５μｍ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、一方その平均層厚が１５
μｍを越えると切刃に欠けやチッピングが発生し易くな
ることから、その平均層厚を０．５〜１５μｍと定め
た。In the coated carbide cutting tool of the present invention, the tough coating layer, the adhesive intermediate coating layer,
The reason why the average thickness of the wear-resistant coating layer is limited as described above will be described. (A) Tough coating layer If the average layer thickness is less than 0.5 μm, desired excellent toughness cannot be secured, and as a result, chipping or chipping (micro chipping) tends to occur on the cutting edge. If the layer thickness exceeds 15 μm, high heat generated during cutting will cause thermoplastic deformation, causing uneven wear on the cutting edge, and this will cause rapid progress of wear. Was determined to be 0.5 to 15 μm. (B) Adhesive intermediate coating layer If the average layer thickness is less than 0.1 μm, it is not possible to secure strong adhesiveness between the tough coating layer and the wear-resistant coating layer. When the layer thickness exceeds 10 μm,
Since the entire physical vapor deposition coating layer promotes embrittlement and is likely to cause chipping or chipping of the cutting edge, the average layer thickness is set to 0.1.
It was determined as 1 to 10 μm. (C) Abrasion-resistant coating layer If the average layer thickness is less than 0.5 μm, the desired excellent wear resistance cannot be secured, while the average layer thickness is 15 μm.
If the thickness exceeds μm, chipping and chipping of the cutting edge easily occur, so the average layer thickness is set to 0.5 to 15 μm.
【０００８】また、上記耐摩耗性被覆層におけるＡｌの
Ｔａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒによる置換含有割
合を５〜２０原子％としたのは、その含有割合が５原子
％未満では前記耐摩耗性被覆層に上記密着性中間被覆層
との間に十分な密着性を確保することのできる圧縮残留
応力を形成することができず、一方その含有割合が２０
原子％を越えると圧縮残留応力が大きくなりすぎて自己
破壊を起こし易くなるという理由にもとづくものであ
る。さらに、上記耐摩耗性被覆層の上に、必要に応じて
ＴｉＮ層を０．１〜２μｍの平均層厚で形成してもよ
く、これはＴｉＮ層が黄金色の色調を有し、この色調に
よって切削工具の使用前と使用後の識別が容易になると
いう理由からで、この場合その層厚が０．１μｍ未満で
は前記色調の付与が不十分であり、一方前記色調の付与
は２μｍまでの平均層厚で十分である。[0008] Further, the substitution content ratio of Al by Ta, V, Nb, W, Mo and Cr in the wear-resistant coating layer is set to 5 to 20 at.% If the content ratio is less than 5 at. A compressive residual stress that can ensure sufficient adhesion between the wear-resistant coating layer and the adhesive intermediate coating layer cannot be formed.
This is based on the reason that if the content exceeds atomic%, the compressive residual stress becomes too large and self-destruction easily occurs. Further, a TiN layer may be formed on the abrasion-resistant coating layer, if necessary, with an average thickness of 0.1 to 2 μm, since the TiN layer has a golden color tone. In this case, the color tone is insufficiently applied when the thickness of the cutting tool is less than 0.1 μm, while the color tone is insufficiently applied up to 2 μm. An average layer thickness is sufficient.
【０００９】[0009]
【発明の実施の形態】ついで、この発明の被覆超硬切削
工具を実施例により具体的に説明する。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、Ｎｂ
Ｃ粉末、Ｃｒ3 Ｃ2 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、ボールミルで７２時間湿式混合
し、乾燥した後、１．５×１０8Ｐａの圧力で圧粉体に
プレス成形し、この圧粉体を真空中、温度：１４００℃
に１時間保持の条件で焼結し、焼結後、切刃部分にＲ：
０．０５のホーニング加工を施してＩＳＯ規格・ＳＰＧ
Ａ１２０４０８のチップ形状をもったＷＣ基超硬合金製
の超硬工具基体Ａ１〜Ａ８を形成した。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Ｔ
ｉＣＮ（質量比でＴｉＣ／ＴｉＮ＝５０／５０）粉末、
Ｍｏ2 Ｃ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、９．８×１０
7Ｐａの圧力で圧粉体にプレス成形し、この圧粉体を
１．３×１０3Ｐａ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：
０．０３のホーニング加工を施してＩＳＯ規格・ＣＮＭ
Ｇ１２０４０６のチップ形状をもったＴｉＣＮ基サーメ
ット製の超硬工具基体Ｂ１〜Ｂ６を形成した。DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the coated carbide cutting tool of the present invention will be specifically described with reference to examples. WC powder having an average particle diameter of 1 to 3 μm,
TiC powder, ZrC powder, VC powder, TaC powder, Nb
A C powder, a Cr 3 C 2 powder, a TiN powder, a TaN powder, and a Co powder 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. It is press-molded into a green compact at a pressure of 1.5 × 10 8 Pa, and the green compact is heated in a vacuum at a temperature of 1400 ° C.
For 1 hour, and after sintering, add R:
Honing process of 0.05 and ISO standard / SPG
Carbide tool bases A1 to A8 made of a WC-based cemented carbide having a chip shape of A120408 were formed. In addition, as raw material powders, T powder having an average particle size of 0.5 to 2 μm is used.
iCN (TiC / TiN = 50/50 by mass ratio) powder,
Mo 2 C powder, ZrC powder, NbC powder, TaC powder,
WC powder, Co powder, and Ni powder were prepared, and these raw material powders were blended in the composition shown in Table 2, wet-mixed in a ball mill for 24 hours, and dried, and then 9.8 × 10
A green compact is press-molded at a pressure of 7 Pa, and the green compact is pressed in a nitrogen atmosphere of 1.3 × 10 3 Pa at a temperature of 1540 ° C.
For 1 hour, and after sintering, add R:
Applying honing process of 0.03, ISO standard, CNM
Carbide tool bases B1 to B6 made of TiCN-based cermet having a chip shape of G120406 were formed.
【００１０】ついで、これら超硬工具基体Ａ１〜Ａ８お
よびＢ１〜Ｂ６を、アセトン中で超音波洗浄し、乾燥し
た状態で、それぞれ図１に示されるアークイオンプレー
ティング装置に装入し、一方カソード電極（蒸発源）と
して種々の成分組成をもったＴｉ−Ａｌ合金を装着し、
装置内を排気して１．３×１０-3Ｐａの真空に保持しな
がら、ヒーターで装置内を５００℃に加熱した後、Ａｒ
ガスを装置内に導入して２．５ＰａのＡｒ雰囲気とし、
この状態で超硬工具基体に−８００ｖのパルスバイアス
電圧を印加して超硬工具基体表面をＡｒガスボンバート
洗浄し、ついで装置内に反応ガスとして窒素ガス、また
は窒素ガスとメタンガスを導入して２．５Ｐａの反応雰
囲気とすると共に、前記超硬工具基体に印加するパルス
バイアス電圧を−２００ｖに下げて、前記カソード電極
とアノード電極との間にアーク放電を発生させ、もって
前記超硬工具基体Ａ１〜Ａ８およびＢ１〜Ｂ６のそれぞ
れの表面に、表３、４に示される目標組成および目標層
厚の強靭性被覆層を形成することにより従来被覆超硬工
具基体１〜２２をそれぞれ製造した。[0010] Then, the carbide tool bases A1 to A8 and B1 to B6 are ultrasonically cleaned in acetone and dried, and each is charged into an arc ion plating apparatus shown in FIG. Ti-Al alloys with various component compositions are installed as electrodes (evaporation sources),
While the inside of the apparatus was evacuated and kept at a vacuum of 1.3 × 10 −3 Pa, the inside of the apparatus was heated to 500 ° C. with a heater.
A gas was introduced into the apparatus to make an Ar atmosphere of 2.5 Pa,
In this state, a pulse bias voltage of -800 V is applied to the cemented carbide substrate to wash the surface of the cemented carbide substrate with Ar gas bombardment. Then, nitrogen gas or a mixture of nitrogen gas and methane gas is introduced into the apparatus as a reaction gas. In addition to the reaction atmosphere of 0.5 Pa, the pulse bias voltage applied to the cemented carbide tool base was reduced to -200 V to generate an arc discharge between the cathode electrode and the anode electrode. A8 and A1 and B1 to B6 were each formed with a tough coating layer having a target composition and a target layer thickness shown in Tables 3 and 4 to produce conventionally coated cemented carbide tool substrates 1 to 22, respectively.
【００１１】ついで、これら従来被覆超硬切削工具１〜
２２のそれぞれの表面に、同じく図１のアークイオンプ
レーティング装置にて、カソード電極（蒸発源）とし
て、密着性中間被覆層形成には種々の成分組成をもった
Ｔｉ−Ａｌ合金、また耐摩耗性被覆層形成にはＴａ、
Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒのうちの１種または２種
以上を所定量含有したＡｌ−（Ｔａ，Ｖ，Ｎｂ，Ｗ，Ｍ
ｏ，Ｃｒ）合金を装着し、装置内を排気して１．３×１
０-3Ｐａの真空に保持しながら、ヒーターで装置内を６
２０〜７２０℃の範囲内の所定の温度に加熱した状態
で、超硬基体に印加するパルスバイアス電圧を−７００
Ｖとし、ついで装置内に反応ガスとして、密着性中間被
覆層形成にはメタンガスと酸素ガス、あるいはメタンガ
スと窒素ガスと酸素ガス、また耐摩耗性被覆層形成には
酸素ガスを導入しながら、前記カソード電極とアノード
電極との間にアーク放電を発生させ、もって表５〜７に
示される目標組成および目標層厚の密着性中間被覆層お
よび耐摩耗性被覆層を形成することにより本発明被覆超
硬切削工具１〜２２をそれぞれ製造した。Next, the conventional coated carbide cutting tools 1 to 1
On the surface of each of the samples No. 22, a Ti-Al alloy having various component compositions for forming an adhesive intermediate coating layer as a cathode electrode (evaporation source) by the arc ion plating apparatus of FIG. Ta for forming the conductive coating layer,
Al- (Ta, V, Nb, W, M) containing a predetermined amount of one or more of V, Nb, W, Mo and Cr.
o, Cr) alloy, and 1.3 × 1
0 while maintaining a vacuum of -3 Pa, the inside of the apparatus with a heater 6
While heating to a predetermined temperature within the range of 20 to 720 ° C., the pulse bias voltage applied to the carbide substrate is set to −700.
V, and then as a reaction gas in the apparatus, while introducing methane gas and oxygen gas, or methane gas, nitrogen gas, and oxygen gas for forming the adhesive intermediate coating layer, and introducing oxygen gas for forming the wear-resistant coating layer, An arc discharge is generated between the cathode electrode and the anode electrode to form an adhesive intermediate coating layer and a wear-resistant coating layer having the target compositions and target layer thicknesses shown in Tables 5 to 7, whereby the coating of the present invention is obtained. Hard cutting tools 1 to 22 were manufactured respectively.
【００１２】上記本発明被覆超硬切削工具１〜２２の耐
摩耗性被覆層を構成するＡｌ2 Ｏ3主体層におけるＴ
ａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒの含有量を、エネル
ギー分散型Ｘ線測定装置を用いて定量分析したところ、
表７の目標含有量と実質的に同じ含有量を示し、また前
記Ａｌ2 Ｏ3 主体層の圧縮残留応力をＸ線応力測定法を
用いて測定したところ、同じく表７に示される結果を示
した。さらに各種被覆層の組成および層厚についてもオ
ージェ分光分析法および光学顕微鏡にて測定したとこ
ろ、表３〜７の目標組成および目標層厚と実質的に同じ
組成および平均層厚（任意５ヶ所測定の平均値との比
較）を示した。[0012] The T 2 in the Al 2 O 3 main layer constituting the wear-resistant coating layer of the coated carbide cutting tools 1 to 22 of the present invention.
When the contents of a, V, Nb, W, Mo and Cr were quantitatively analyzed using an energy dispersive X-ray measuring apparatus,
The content was substantially the same as the target content in Table 7, and the compressive residual stress of the Al 2 O 3 main layer was measured using an X-ray stress measurement method. Was. Furthermore, the composition and layer thickness of each coating layer were also measured by Auger spectroscopy and an optical microscope, and the compositions and average layer thicknesses substantially the same as the target compositions and target layer thicknesses in Tables 3 to 7 (measured at five arbitrary locations) (Comparison with the average value).
【００１３】ついで、この結果得られた各種の被覆超硬
切削工具のうち、本発明被覆超硬切削工具１〜１６およ
び従来被覆超硬切削工具１〜１６について、 被削材：ＪＩＳ・Ｓ５０Ｃの長さ方向等間隔４本縦溝入
り丸棒、 切削速度：２８０ｍ／min.、 送り：０．３ｍｍ／rev.、 切込み：２．８ｍｍ、 切削時間：１０分、 の条件での炭素鋼の乾式断続高切込み切削試験、およ
び、 被削材：ＪＩＳ・ＳＮＣＭ４４０の長さ方向等間隔４本
縦溝入り丸棒、 切削速度：３００ｍ／min.、 送り：０．４３ｍｍ／rev.、 切込み：１．５ｍｍ、 切削時間：１０分、 の条件での合金鋼の乾式断続高送り切削試験を行ない、
また本発明被覆超硬切削工具１７〜２２および従来被覆
超硬切削工具１７〜２２については、 被削材：ＪＩＳ・ＳＵＳ３０４の長さ方向等間隔４本縦
溝入り丸棒、 切削速度：３３０ｍ／min.、 送り：０．３ｍｍ／rev.、 切込み：２．８ｍｍ、 切削時間：１０分、 の条件でのステンレス鋼の乾式断続高切込み切削試験、
および、 被削材：ＪＩＳ・ＳＮＣＭ４４０の長さ方向等間隔４本
縦溝入り丸棒、 切削速度：３８０ｍ／min.、 送り：０．４６ｍｍ／rev.、 切込み：１．５ｍｍ、 切削時間：１０分、 の条件での合金鋼の乾式断続高送り切削試験を行ない、
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, among the various coated carbide cutting tools obtained as a result, the coated carbide cutting tools 1 to 16 of the present invention and the conventional coated carbide cutting tools 1 to 16 are described below. Work material: JIS S50C Round bar with four longitudinal grooves at equal intervals in the longitudinal direction, Cutting speed: 280 m / min., Feed: 0.3 mm / rev., Depth of cut: 2.8 mm, Cutting time: 10 min. Intermittent high-cut cutting test and work material: JIS SNCM440 lengthwise round bar with four longitudinal grooves, cutting speed: 300 m / min., Feed: 0.43 mm / rev., Depth of cut: 1. 5mm, cutting time: 10 minutes, dry intermittent high feed cutting test of alloy steel under the following conditions:
The coated carbide cutting tools 17 to 22 of the present invention and the conventionally coated carbide cutting tools 17 to 22 are as follows: Work material: JIS SUS304, four longitudinally spaced round bars at regular intervals in the longitudinal direction, Cutting speed: 330 m / min., feed: 0.3 mm / rev., depth of cut: 2.8 mm, cutting time: 10 minutes, dry intermittent high depth cutting test of stainless steel under the following conditions:
And Work material: JIS SNCM440 lengthwise equally spaced round bar with four longitudinal grooves, Cutting speed: 380 m / min., Feeding: 0.46 mm / rev., Cutting depth: 1.5 mm, Cutting time: 10 And a dry intermittent high feed cutting test of alloy steel under the conditions of
In each cutting test, the flank wear width of the cutting edge was measured.
Table 8 shows the measurement results.
【００１４】[0014]
【表１】 [Table 1]
【００１５】[0015]
【表２】 [Table 2]
【００１６】[0016]
【表３】 [Table 3]
【００１７】[0017]
【表４】 [Table 4]
【００１８】[0018]
【表５】 [Table 5]
【００１９】[0019]
【表６】 [Table 6]
【００２０】[0020]
【表７】 [Table 7]
【００２１】[0021]
【表８】 [Table 8]
【００２２】[0022]
【発明の効果】表３〜８に示される結果から、本発明被
覆超硬切削工具１〜２２は、いずれも耐摩耗性被覆層を
構成するＡｌ2 Ｏ3 主体層がＡｌに比してイオン半径の
大きいＴａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒのうちの１
種以上を置換含有し、これによって高い圧縮残留応力を
保持するようになって、密着性中間被覆層を構成する
（Ｔｉ，Ａｌ）ＣＯ層および（Ｔｉ，Ａｌ）ＣＮＯ層に
強固に密着し、一方前記密着性中間被覆層は上記の強靭
性被覆層を構成する（Ｔｉ，Ａｌ）Ｎ層および（Ｔｉ，
Ａｌ）ＣＮ層に対しも強固に密着するので、鋼の断続切
削を高切込みおよび高送りの重切削条件で行っても前記
Ａｌ2 Ｏ3 主体層に剥離の発生なく、すぐれた耐摩耗性
を発揮するのに対して、従来被覆超硬切削工具１〜２２
は、いずれもこれの強靭性被覆層の耐摩耗性不足が原因
で、上記のような苛酷な条件下では摩耗進行が速いこと
が明らかである。上述のように、この発明の被覆超硬切
削工具は、耐摩耗性被覆層を構成するＡｌ2 Ｏ3 主体層
のもつすぐれた耐摩耗性および密着性中間被覆層に対す
るすぐれた密着性、さらに超硬工具基体と強靭性被覆
層、並びに強靭性被覆層と密着性中間被覆層との間に確
保される良好な密着性によって、通常の条件での各種鋼
の連続切削および断続切削は勿論のこと、きわめて苛酷
な切削条件である断続切削を高切り込みおよび高送りの
重切削条件で行っても前記Ａｌ2 Ｏ3 主体層に剥離の発
生なく、かつ切刃に欠けやチッピングの発生もなく、す
ぐれた耐摩耗性を示し、長期に亘ってすぐれた切削性能
を発揮するものであり、切削加工の省エネ化および省力
化に十分満足に対応できるものである。According to the results shown in Tables 3 to 8, in the coated carbide cutting tools 1 to 22 of the present invention, the Al 2 O 3 main layer constituting the wear-resistant coating layer has a higher ion content than Al. One of Ta, V, Nb, W, Mo and Cr having a large radius
The compound contains more than one species, thereby maintaining a high compressive residual stress, and firmly adheres to the (Ti, Al) CO layer and the (Ti, Al) CNO layer constituting the adhesive intermediate coating layer, On the other hand, the adhesive intermediate coating layer comprises the (Ti, Al) N layer and the (Ti,
Al) It adheres strongly to the CN layer, so that even when intermittent cutting of steel is performed under high cutting and high feed heavy cutting conditions, the Al 2 O 3 main layer does not peel and excellent wear resistance is obtained. In contrast to conventional coated carbide cutting tools 1-22
It is evident that in any case, the wear progresses rapidly under the severe conditions as described above due to the lack of wear resistance of the tough coating layer. As described above, the coated carbide cutting tool according to the present invention provides excellent wear resistance and adhesion of the Al 2 O 3 main layer constituting the wear resistant coating layer, and excellent adhesion to the intermediate coating layer. Due to the good adhesion secured between the hard tool base and the tough coating layer, and between the tough coating layer and the adhesive intermediate coating layer, continuous cutting and intermittent cutting of various steels under normal conditions, as well as Even when intermittent cutting, which is extremely severe cutting conditions, is performed under high cutting and high feed heavy cutting conditions, the Al 2 O 3 main layer does not peel off, and the cutting edge does not chip or chip. It has excellent wear resistance and exhibits excellent cutting performance over a long period of time, and can sufficiently cope with energy saving and labor saving in cutting.
【図１】アークイオンプレーティング装置の概略説明図
である。FIG. 1 is a schematic explanatory view of an arc ion plating apparatus.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.7 識別記号 ＦＩ テーマコート゛(参考） Ｃ２２Ｃ 29/02 Ｃ２２Ｃ 29/02 Ａ 29/04 29/04 Ａ Ｚ 29/08 29/08 29/12 29/12 Ｚ 29/16 29/16 Ｈ Ｃ２３Ｃ 14/06 Ｃ２３Ｃ 14/06 Ｐ 14/16 14/16 Ｂ ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 7 Identification symbol FI theme coat ゛ (Reference) C22C 29/02 C22C 29/02 A 29/04 29/04 AZ 29/08 29/08 29/12 29 / 12 Z 29/16 29/16 H C23C 14/06 C23C 14/06 P 14/16 14/16 B
Claims (1)
化チタン基サーメットで構成された工具基体の表面に、
ＴｉとＡｌの複合窒化物層および複合炭窒化物層のうち
の１種の単層または２種の複層からなる強靭性被覆層を
０．５〜１５μｍの平均層厚で物理蒸着してなる表面被
覆超硬合金製切削工具において、 上記強靭性被覆層の表面に、さらに０．１〜１０μｍの
平均層厚を有するＴｉとＡｌの複合炭酸化物層および複
合炭窒酸化物層のうちの１種の単層または２種の複層か
らなる密着性中間被覆層を介して、 酸化アルミニウムのもつ結晶構造を保持したままで、Ａ
ｌの一部をＡｌとの合量に占める割合で５〜２０原子％
のＴａ、Ｖ、Ｎｂ、Ｗ、ＭｏおよびＣｒのうちの１種ま
たは２種以上で置換固溶してなる酸化アルミニウム主体
層からなる耐摩耗性被覆層を０．５〜１５μｍの平均層
厚で物理蒸着したことを特徴とする耐摩耗性のすぐれた
表面被覆超硬合金製切削工具。1. A tool base comprising a tungsten carbide based cemented carbide or a titanium carbonitride based cermet,
A tough coating layer composed of one single layer or two or more composite layers of a composite nitride layer and a composite carbonitride layer of Ti and Al is physically vapor-deposited with an average layer thickness of 0.5 to 15 μm. In a cutting tool made of a surface-coated cemented carbide, one of a composite carbonate layer of Ti and Al and a composite carbonitride layer having an average layer thickness of 0.1 to 10 μm is further provided on the surface of the tough coating layer. While maintaining the crystal structure of aluminum oxide through an adhesive intermediate coating layer composed of a single kind of layer or two kinds of multiple layers,
5 to 20 atomic% in a proportion of l to the total amount with Al
A wear-resistant coating layer composed of an aluminum oxide-based layer obtained by substituting one or more of Ta, V, Nb, W, Mo and Cr with a mean thickness of 0.5 to 15 μm. Cutting tool made of cemented carbide with excellent wear resistance, characterized by physical vapor deposition.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000140658A JP2001322006A (en) | 2000-05-12 | 2000-05-12 | Surface coated cemented carbide cutting tool with excellent wear resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000140658A JP2001322006A (en) | 2000-05-12 | 2000-05-12 | Surface coated cemented carbide cutting tool with excellent wear resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2001322006A true JP2001322006A (en) | 2001-11-20 |
Family
ID=18647911
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2000140658A Pending JP2001322006A (en) | 2000-05-12 | 2000-05-12 | Surface coated cemented carbide cutting tool with excellent wear resistance |
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| Country | Link |
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| JP (1) | JP2001322006A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003089172A1 (en) * | 2002-04-19 | 2003-10-30 | Mitsubishi Materials Corporation | Cubic boron nitride base ultra-high pressure sintered material cutting tip |
| US7426337B2 (en) | 2003-02-28 | 2008-09-16 | Matsushita Electric Industrial Co., Ltd. | Recording medium, reproduction apparatus, recording method, program, and reproduction method |
| RU2485208C2 (en) * | 2011-08-04 | 2013-06-20 | Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Нижегородский государственный технический университет им. Р.Е. Алексеева" (НГТУ) | Cutting plate manufacturing method |
| RU2495950C1 (en) * | 2012-06-26 | 2013-10-20 | Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Ульяновский государственный технический университет" | Method of producing sandwiched coating for cutting tool |
-
2000
- 2000-05-12 JP JP2000140658A patent/JP2001322006A/en active Pending
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2003089172A1 (en) * | 2002-04-19 | 2003-10-30 | Mitsubishi Materials Corporation | Cubic boron nitride base ultra-high pressure sintered material cutting tip |
| US7112235B2 (en) | 2002-04-19 | 2006-09-26 | Mitsubishi Materials Corporation | Cubic boron nitride base ultra-high pressure sintered material cutting tip |
| US7426337B2 (en) | 2003-02-28 | 2008-09-16 | Matsushita Electric Industrial Co., Ltd. | Recording medium, reproduction apparatus, recording method, program, and reproduction method |
| US7466903B2 (en) | 2003-02-28 | 2008-12-16 | Panasonic Corporation | Recording medium, reproduction apparatus, recording method, program, and reproduction method |
| US7499629B2 (en) | 2003-02-28 | 2009-03-03 | Panasonic Corporation | Recording medium, reproduction apparatus, recording method, program, and reproduction method |
| RU2485208C2 (en) * | 2011-08-04 | 2013-06-20 | Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Нижегородский государственный технический университет им. Р.Е. Алексеева" (НГТУ) | Cutting plate manufacturing method |
| RU2495950C1 (en) * | 2012-06-26 | 2013-10-20 | Федеральное государственное бюджетное образовательное учреждение высшего профессионального образования "Ульяновский государственный технический университет" | Method of producing sandwiched coating for cutting tool |
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