JP2002200502A - Surface coated cemented carbide throw away tip exerting excellent wear resistance by high speed cutting - Google Patents
Surface coated cemented carbide throw away tip exerting excellent wear resistance by high speed cuttingInfo
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- JP2002200502A JP2002200502A JP2000397081A JP2000397081A JP2002200502A JP 2002200502 A JP2002200502 A JP 2002200502A JP 2000397081 A JP2000397081 A JP 2000397081A JP 2000397081 A JP2000397081 A JP 2000397081A JP 2002200502 A JP2002200502 A JP 2002200502A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- carbide
- cemented carbide
- vapor deposition
- hard coating
- 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.)
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、炭化タングステ
ン基超硬合金基体（以下、超硬基体という）がすぐれた
高温強度を有すると共に、硬質被覆層がすぐれた高温強
度と高温硬さを有し、したがって高熱発生を伴なう鋼や
鋳鉄などの高速切削加工に用いた場合に、すぐれた耐摩
耗性を発揮する表面被覆超硬合金製スローアウエイチッ
プ（以下、被覆超硬チップという）に関するものであ
る。The present invention relates to a tungsten carbide-based cemented carbide substrate (hereinafter referred to as a cemented carbide substrate) having excellent high-temperature strength and a hard coating layer having excellent high-temperature strength and high-temperature hardness. Therefore, when used for high-speed cutting of steel or cast iron with high heat generation, it relates to a throw-away tip made of a surface-coated cemented carbide that exhibits excellent wear resistance (hereinafter referred to as a coated carbide tip). It is.
【０００２】[0002]
【従来の技術】従来、一般に、被覆超硬チップが、例え
ば図１（ａ）に概略斜視図で、同（ｂ）に概略縦断面図
で示される形状を有し、バイトの先端部に着脱自在に取
り付けて各種の鋼や鋳鉄などの被削材の旋削加工や平削
り加工を行なうのに用いたり、さらに正面フライス工具
のカッター正面に着脱自在に取り付けて、前記被削材の
面削加工や溝加工、さらに肩加工などに用いられること
は良く知られるところである。また上記被覆超硬チップ
として、超硬基体の表面に、ＴｉとＡｌの複合窒化物
［以下、（Ｔｉ，Ａｌ）Ｎで示す］で構成された硬質被
覆層を０．５〜１０μｍの平均層厚で形成してなる被覆
超硬チップも知られている。2. Description of the Related Art Conventionally, a coated cemented carbide tip generally has a shape shown, for example, in a schematic perspective view in FIG. 1A and a schematic longitudinal sectional view in FIG. Used for turning and planing of various materials such as steel and cast iron, and can be freely attached to and detachable from the front of the cutter of a face milling tool to be able to face-cut the material. It is well-known that it is used for groove machining, groove machining, and shoulder machining. Further, as the coated carbide chip, a hard coating layer composed of a composite nitride of Ti and Al [hereinafter, referred to as (Ti, Al) N] is formed on a surface of a carbide substrate in an average layer of 0.5 to 10 μm. Coated carbide tips formed with a large thickness are also known.
【０００３】さらに、上記の被覆超硬チップの硬質被覆
層である（Ｔｉ，Ａｌ）Ｎ層が、例えば図２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、例えば雰
囲気を３Ｐａの真空として、５００℃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、例
えば電圧：３５Ｖ、電流：９０Ａの条件でアーク放電を
発生させ、同時に装置内に反応ガスとして窒素ガスを導
入し、一方超硬基体には、例えばー２００Ｖのバイアス
電圧を印加する条件で形成されることも知られている。[0003] Furthermore, the (Ti, Al) N layer, which is a hard coating layer of the coated superhard tip, is an arc ion plating apparatus which is a kind of physical vapor deposition apparatus schematically shown in FIG. The heater is used to heat the inside of the apparatus to a temperature of 500 ° C., for example, by setting the atmosphere to a vacuum of 3 Pa, and the anode electrode and the cathode electrode (evaporation source) on which a Ti—Al alloy having a predetermined composition is set. For example, an arc discharge is generated under the conditions of, for example, a voltage of 35 V and a current of 90 A, and at the same time, nitrogen gas is introduced as a reaction gas into the apparatus, while a bias voltage of, for example, -200 V is applied to the cemented carbide substrate. It is also known to be formed.
【０００４】[0004]
【発明が解決しようとする課題】一方、近年の切削加工
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、切削加工は切削機械の高性能化
とも相俟って高速化の傾向にあるが、従来提案されてい
る各種の被覆超硬チップにおいては、これを鋼や鋳鉄な
どの通常の条件での切削加工に用いた場合には問題はな
いが、これを高速切削条件で用いると、切削加工時に発
生する高熱によって、特に切刃のすくい面と逃げ面の交
わる切刃稜線部に偏摩耗の原因となる熱塑性変形が発生
するようになるばかりでなく、前記切刃稜線部の高温硬
さの著しい低下とも相俟って切刃の摩耗進行が促進し、
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。On the other hand, in recent years, there has been a strong demand for labor saving, energy saving, and further cost reduction in cutting work, and with this, cutting work has been performed at high speeds in conjunction with high performance of cutting machines. Although there is no problem with the various types of coated carbide tips that have been proposed in the past when using them for cutting under ordinary conditions such as steel or cast iron, this is not a problem. When used under the conditions, the high heat generated during the cutting process causes not only the cutting edge ridge portion where the rake face and the flank face of the cutting edge intersect to cause thermoplastic deformation causing uneven wear, but also the cutting edge. Along with the remarkable decrease in the high-temperature hardness of the ridge, the wear progress of the cutting edge is promoted,
As a result, at present, the service life is reached in a relatively short time.
【０００５】[0005]
【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、すぐれた高温強度と高温硬さを
具備した被覆超硬チップを開発すべく研究を行った結
果、 （ａ）原料粉末として、炭化タングステン（以下、ＷＣ
で示す）粉末、炭化クロム（以下、Ｃｒ3Ｃ2で示す）粉
末、炭化バナジウム（以下、ＶＣで示す）粉末、および
Ｃｏ粉末を用いて、配合組成を、質量％で（以下、％は
質量％を示す）、Ｃｏ：５〜１４％、Ｃｒ3Ｃ2：０．１
〜２％、ＶＣ：０．１〜２％、ＷＣ：残り、としてなる
圧粉体の焼結体においては、これを構成する結合相が、
焼結時にＣｏ中にＣｒ3Ｃ2およびＶＣが固溶し、さらに
Ｃｒ3Ｃ2の固溶によって硬質相を形成するＷＣの一部の
固溶も促進されることから、Ｃｏ−Ｃｒ−Ｖ−Ｗ系合金
で構成されるようになり、このＣｏ−Ｃｒ−Ｖ−Ｗ系合
金はすぐれた高温強度をもつことから、焼結体の高温強
度が向上するようになること。Means for Solving the Problems Accordingly, the present inventors have
From the above viewpoints, we conducted research to develop coated carbide tips having excellent high-temperature strength and high-temperature hardness. (A) As a raw material powder, tungsten carbide (hereinafter referred to as WC)
), Chromium carbide (hereinafter, referred to as Cr 3 C 2 ) powder, vanadium carbide (hereinafter, referred to as VC) powder, and Co powder, and the composition is expressed in mass% (hereinafter,% is mass). %), Co: 5 to 14%, Cr 3 C 2 : 0.1
-2%, VC: 0.1-2%, WC: Remaining, in the sintered compact of the compact,
Since Cr 3 C 2 and VC form a solid solution in Co during sintering, and the solid solution of Cr 3 C 2 also promotes the solid solution of a part of WC forming a hard phase, so that Co—Cr—V -W-based alloy, and this Co-Cr-V-W-based alloy has excellent high-temperature strength, so that the high-temperature strength of the sintered body is improved.
【０００６】（ｂ）上記（ａ）の焼結体を基体（超硬基
体）とし、これの表面に硬質被覆層として物理蒸着法を
用いて、組成式：（Ｔｉ1-XＡｌX）Ｎ（ただし、Ｘは、
原子比で０．３〜０．７）を有する（Ｔｉ，Ａｌ）Ｎ層
を形成すると、この（Ｔｉ，Ａｌ）Ｎ層はすぐれた高温
強度を備えたものとなること。(B) The sintered body of (a) is used as a substrate (ultra-hard substrate), and a hard coating layer is formed on the surface of the substrate by physical vapor deposition using a composition formula: (Ti 1-x Al x ) N (However, X is
When a (Ti, Al) N layer having an atomic ratio of 0.3 to 0.7) is formed, the (Ti, Al) N layer has excellent high-temperature strength.
【０００７】（ｃ）上記（ｂ）の（Ｔｉ，Ａｌ）Ｎ層
は、上記の通りすぐれた高温強度をもつものの、高速切
削加工時の高温下で十分な高温硬さを維持するものでは
ないが、これを内側層とし、この内側層の上に外側層と
して、反応ガス雰囲気温度を７５０〜８５０℃とした中
温化学蒸着法で結晶構造がκ型の酸化アルミニウム（以
下、Ａｌ2Ｏ3で示す）層を形成すると、このκ型Ａｌ2
Ｏ3層は高い高温硬さもつことから、前期内側層の（Ｔ
ｉ，Ａｌ）Ｎ層と前記外側層のκ型Ａｌ2Ｏ3層との積層
からなる硬質被覆層はすぐれた高温強度と高温硬さを具
備するようになること。(C) Although the (Ti, Al) N layer of (b) has excellent high-temperature strength as described above, it does not maintain sufficient high-temperature hardness at high temperatures during high-speed cutting. However, by using this as an inner layer, and as an outer layer on this inner layer, aluminum oxide (hereinafter referred to as Al 2 O 3) having a crystal structure of κ type by a medium temperature chemical vapor deposition method with a reaction gas atmosphere temperature of 750 to 850 ° C. Layer), this κ-type Al 2
Since the O 3 layer has a high temperature hardness, the (T
A hard coating layer comprising a lamination of an i, Al) N layer and the κ-type Al 2 O 3 layer as the outer layer has excellent high-temperature strength and high-temperature hardness.
【０００８】（ｄ）したがって、上記（ａ）の超硬基体
の表面に上記（ｂ）および（ｃ）の硬質被覆層を蒸着形
成してなる被覆超硬チップは、前記超硬基体によってす
ぐれた耐熱塑性変形性を具備し、かつ前記（Ｔｉ，Ａ
ｌ）Ｎ層とκ型Ａｌ2Ｏ3層の積層からなる硬質被覆層に
よってすぐれた高温強度と高温硬さをもつようになるこ
とから、これを高熱発生を伴なう高速切削加工に用いて
も偏摩耗が著しく抑制され、長期に亘ってすぐれた耐摩
耗性を発揮すること。(D) Therefore, the coated superhard chip formed by vapor-depositing the hard coating layers of (b) and (c) on the surface of the superhard substrate of (a) is excellent by the superhard substrate. It has heat-resistant plastic deformation property and the (Ti, A
l) Since a hard coating layer composed of a laminate of an N layer and a κ-type Al 2 O 3 layer has excellent high-temperature strength and high-temperature hardness, it is used for high-speed cutting with high heat generation. In addition, uneven wear is remarkably suppressed, and excellent wear resistance is exhibited over a long period of time.
【０００９】（ｅ）上記（ａ）で示した原料粉末に加え
て、さらに原料粉末として、炭化チタン(以下、ＴｉＣ
で示す)粉末、炭化ニオブ(以下、ＮｂＣで示す)粉末、
炭化タンタル(以下、ＴａＣで示す)粉末、ＮｂとＴａの
複合炭化物［以下、（Ｎｂ，Ｔａ）Ｃで示す］粉末、お
よびＴｉとＷの複合炭化物［以下、（Ｔｉ，Ｗ）Ｃで示
す］粉末を用いて、配合組成を、Ｃｏ：５〜１４％、Ｃ
ｒ3Ｃ2：０．１〜２％、ＶＣ：０．１〜２％、ＴｉＣ、
ＮｂＣ、ＴａＣ、（Ｎｂ，Ｔａ）Ｃ、および（Ｔｉ，
Ｗ）Ｃのうちの１種又は２種以上：０．５〜２５％、Ｗ
Ｃ：残り、としてなる圧粉体の焼結体は、硬質相として
存在するようになる上記ＴｉＣ、ＮｂＣ、ＴａＣ、（Ｎ
ｂ，Ｔａ）Ｃ、および（Ｔｉ，Ｗ）Ｃの作用によって一
段と高い高温硬さをもつようになり、したがって、この
焼結体で超硬基体を構成してなる被覆超硬チップは上記
の硬質被覆層の作用とも相俟って、高速切削加工で一層
の耐摩耗性向上が見込めること。以上（ａ）〜（ｅ）に
示される研究結果が得られたのである。(E) In addition to the raw material powder shown in (a), titanium carbide (hereinafter referred to as TiC)
) Powder, niobium carbide (hereinafter, referred to as NbC) powder,
Tantalum carbide (hereinafter referred to as TaC) powder, composite carbide of Nb and Ta [hereinafter referred to as (Nb, Ta) C] powder, and composite carbide of Ti and W [hereinafter referred to as (Ti, W) C] Using powder, the composition was adjusted to 5% to 14% Co, C
r 3 C 2: 0.1~2%, VC: 0.1~2%, TiC,
NbC, TaC, (Nb, Ta) C, and (Ti,
W) One or more of C: 0.5 to 25%, W
C: The remaining sintered body of the compact as the TiC, NbC, TaC, (N
Due to the action of (b, Ta) C and (Ti, W) C, the sintered carbide has a higher high-temperature hardness. Therefore, the coated cemented carbide chip which constitutes a cemented carbide substrate with this sintered body has the above-mentioned hardness. Combined with the function of the coating layer, further improvement in wear resistance can be expected by high-speed cutting. The research results shown in (a) to (e) above were obtained.
【００１０】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、Ｃｏ：５〜１４％、Ｃｒ3Ｃ2：
０．１〜２％、ＶＣ：０．１〜２％、必要に応じてＴｉ
Ｃ、ＮｂＣ、ＴａＣ、（Ｎｂ，Ｔａ）Ｃ、および（Ｔ
ｉ，Ｗ）Ｃのうちの１種又は２種以上：０．５〜２５
％、ＷＣ：残り、からなる配合組成を有する圧粉体の焼
結体で構成された超硬基体の表面に、（ａ）内側層とし
て、０．５〜１０μｍの平均層厚を有し、かつ物理蒸着
法で形成された、組成式：（Ｔｉ1-XＡｌX）Ｎ（ただ
し、原子比で、Ｘは０．３〜０．７を示す）を有する
（Ｔｉ，Ａｌ）Ｎ層、（ｂ）外側層として、０．１〜５
μｍの平均層厚を有し、かつ中温化学蒸着法で形成され
た、κ型Ａｌ2Ｏ3層、以上（ａ）および（ｂ）で構成さ
れた硬質被覆層を形成してなる、高速切削ですぐれた耐
摩耗性を発揮する被覆超硬チップに特徴を有するもので
ある。The present invention has been made on the basis of the above-mentioned results of the research, and has a Co content of 5 to 14% and a Cr 3 C 2 content of:
0.1-2%, VC: 0.1-2%, if necessary, Ti
C, NbC, TaC, (Nb, Ta) C, and (T
i, W) One or more of C: 0.5 to 25
%, WC: on the surface of a cemented carbide substrate composed of a sintered compact of a compact having the remaining composition of (a) having an average layer thickness of 0.5 to 10 μm as an inner layer, A (Ti, Al) N layer formed by physical vapor deposition and having a composition formula: (Ti 1-x Al x ) N (where X represents 0.3 to 0.7 in atomic ratio); (B) 0.1 to 5 as an outer layer
High-speed cutting having an average layer thickness of μm and forming a hard coating layer composed of the κ-type Al 2 O 3 layer and the above (a) and (b) formed by a medium temperature chemical vapor deposition method. The coated carbide tips exhibit excellent wear resistance.
【００１１】つぎに、この発明の被覆超硬チップにおい
て、これを構成する超硬基体（焼結体）の配合組成、硬
質被覆層のうちの内側層のＸ値、さらに硬質被覆層の平
均層厚を上記の通りに限定した理由を説明する。 （１）超硬基体の配合組成 （ａ）Ｃｏ Ｃｏ成分には、焼結性を向上させ、かつ焼結体の常温強
度を向上させる作用があるが、その割合が５％未満で
は、前記作用に所望の向上効果が得られず、一方その割
合が１４％を越えると、焼結体の高温強度に低下傾向が
現われ、切刃に塑性変形が発生し易くなり、この結果摩
耗進行促進の原因となる偏摩耗が切刃に発生するように
なることから、その割合を５〜１４％と定めた。Next, in the coated cemented carbide chip of the present invention, the composition of the cemented carbide substrate (sintered body) constituting the chip, the X value of the inner layer of the hard coating layer, and the average layer of the hard coating layer The reason why the thickness is limited as described above will be described. (1) Composition of Carbide Substrate (a) Co The Co component has the effect of improving the sinterability and improving the room-temperature strength of the sintered body. However, if the desired improvement effect is not obtained, on the other hand, if the ratio exceeds 14%, the high-temperature strength of the sintered body tends to decrease, and plastic deformation tends to occur on the cutting edge, resulting in accelerated wear. Since the uneven wear occurs on the cutting edge, the ratio is set to 5 to 14%.
【００１２】（ｂ）Ｃｒ3Ｃ2およびＶＣ Ｃｒ3Ｃ2およびＶＣ成分には、上記の通り焼結時に結合
相を形成するＣｏ中に共に完全に固溶し、この固溶によ
ってＷＣのＣｏへの固溶も促進して耐熱性のすぐれたＣ
ｏ−Ｃｒ−Ｖ−Ｗ系合金からなる結合相を形成し、もっ
て焼結体の高温強度を向上させるほか、前記Ｃｒ3Ｃ2成
分には硬質相を形成するＷＣの粒成長を抑制して焼結体
の強度低下を防止する作用があるが、Ｃｒ3Ｃ2およびＶ
Ｃのいずれの成分でも、その割合が０．１％未満になる
と、前記作用に所望の向上効果が得られず、一方その割
合がいずれかでも２％を越えると、結合相の常温強度が
低下するようになることから、その割合をそれぞれＣｒ
3Ｃ2：０．１〜２％、ＶＣ：０．１〜２％と定めた。(B) Cr 3 C 2 and VC The Cr 3 C 2 and VC components are completely dissolved in Co, which forms a binder phase at the time of sintering, as described above. Excellent heat resistance by promoting solid solution in C
In addition to forming a binder phase composed of an o-Cr-VW-based alloy, thereby improving the high-temperature strength of the sintered body, the Cr 3 C 2 component suppresses grain growth of WC that forms a hard phase. It has the effect of preventing the reduction in strength of the sintered body but, Cr 3 C 2 and V
When the proportion of any of the components C is less than 0.1%, a desired improvement effect on the above-mentioned effect cannot be obtained. On the other hand, when the proportion of any of the components exceeds 2%, the room-temperature strength of the binder phase decreases. The ratio is changed to Cr
3 C 2: 0.1~2%, VC : defined as 0.1% to 2%.
【００１３】（ｃ）ＴｉＣ、ＮｂＣ、ＴａＣ、（Ｎｂ，
Ｔａ）Ｃ、および（Ｔｉ，Ｗ）Ｃ これらの成分には、硬質相を形成して焼結体の高温硬さ
を向上させる作用があるので、必要に応じて配合される
が、その割合が０．５％未満では、所望の高温硬さ向上
効果が得られず、一方その割合が２５％を越えると、焼
結体の高温強度が急激に低下するようになることから、
その割合を０．５〜２５％と定めた。(C) TiC, NbC, TaC, (Nb,
Ta) C and (Ti, W) C These components have a function of forming a hard phase and improving the high-temperature hardness of the sintered body. Therefore, these components are blended as necessary. If it is less than 0.5%, the desired effect of improving the high-temperature hardness cannot be obtained, while if its proportion exceeds 25%, the high-temperature strength of the sintered body rapidly decreases.
The ratio was determined to be 0.5 to 25%.
【００１４】（２）硬質被覆層のうちの内側層のＸ値 （Ｔｉ，Ａｌ）Ｎ層におけるＡｌは常温強度の高いＴｉ
Ｎに対して耐熱性を付与し、もってすぐれた高温強度を
具備するようにするために固溶するものであり、したが
って組成式：（Ｔｉ1-XＡｌX）ＮのＸ値が０．３未満で
は所望のすぐれた高温強度を確保することができず、一
方その値が０．７を越えると、具備せしめた高温強度が
低下するようになることから、Ｘ値を０．３〜０．７と
定めた。(2) X value of inner layer of hard coating layer Al in (Ti, Al) N layer is Ti having high strength at room temperature.
N is a solid solution in order to impart heat resistance to N and to have excellent high-temperature strength. Therefore, the X value of the composition formula: (Ti 1-x Al x ) N is 0.3 If the value is less than 0.7, a desired excellent high-temperature strength cannot be ensured. On the other hand, if the value exceeds 0.7, the provided high-temperature strength decreases, so that the X value is 0.3 to 0.3%. 7 was determined.
【００１５】（３）硬質被覆層の平均層厚 硬質被覆層の上記内側層を構成する（Ｔｉ，Ａｌ）Ｎ層
の平均層厚を、０．５〜１０μｍとしたのは、その平均
層厚が０．５μｍ未満では、硬質被覆層に所望の高温強
度を付与することができず、この結果切刃にチッピング
（微小欠け）が発生し易くなり、一方その層厚が１０μ
ｍを越えると、切刃における摩耗進行が局部的になり、
これが原因で切刃に欠けが発生し易くなるという理由か
らである。また、同じく外側層を構成するκ型Ａｌ2Ｏ3
層の平均層厚を０．１〜５μｍとしたのは、その層厚が
０．１μｍ未満では硬質被覆層に所望の高温硬さを付与
することができないので、切刃の耐摩耗性に所望の向上
効果が得られず、一方その層厚が５μｍを越えると、切
刃に欠けやチッピングが発生し易くなるという理由によ
るものである。なお、被覆超硬チップの使用前後の識別
を容易にするために、黄金色を有する炭化チタン（Ｔｉ
Ｎ）層を０．１〜３μｍの平均層厚で上記外側層の表面
に蒸着してもよい。(3) Average Layer Thickness of Hard Coating Layer The average layer thickness of the (Ti, Al) N layer constituting the inner layer of the hard coating layer is set to 0.5 to 10 μm because of the average layer thickness Is less than 0.5 μm, the desired high-temperature strength cannot be imparted to the hard coating layer, and as a result, chipping (minute chipping) tends to occur on the cutting edge, while the layer thickness is 10 μm.
m, the wear progress on the cutting edge becomes localized,
This is because the chip is likely to be chipped due to this. The κ-type Al 2 O 3, which also forms the outer layer,
The reason for setting the average layer thickness of the layer to 0.1 to 5 μm is that if the layer thickness is less than 0.1 μm, a desired high-temperature hardness cannot be imparted to the hard coating layer. Is not obtained, while if the layer thickness exceeds 5 μm, chipping and chipping of the cutting edge are likely to occur. In order to facilitate identification of the coated carbide tip before and after use, titanium carbide having a golden color (Ti
N) A layer may be deposited on the surface of the outer layer with an average layer thickness of 0.1 to 3 μm.
【００１６】[0016]
【発明の実施の形態】つぎに、この発明の被覆超硬チッ
プ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：５．５μｍを有する中粗粒ＷＣ粉末、同０．
８μｍの微粒ＷＣ粉末、同２．３μｍのＣｒ3Ｃ2粉末、
同１．２μｍのＶＣ粉末、同１．５μｍのＴｉＣ粉末、
同１．３μｍのＴａＣ粉末、同１．２μｍのＮｂＣ粉
末、同１．０μｍの（Ｔａ，Ｎｂ）Ｃ［質量比で、Ｔａ
Ｃ／ＮｂＣ＝５０／５０］粉末、同１．０μｍの（Ｔ
ｉ，Ｗ）Ｃ［質量比で、ＴｉＣ／ＷＣ＝７０／３０］粉
末、おとび同１．８μｍのＣｏ粉末を用意し、これら原
料粉末をそれぞれ表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、１００ＭＰａの圧力で所定形
状の圧粉体にプレス成形し、これらの圧粉体を、６Ｐａ
の真空雰囲気中、７℃／分の昇温速度で１３７０〜１４
７０℃の範囲内の所定の温度に昇温し、この温度に１時
間保持後、炉冷の条件で焼結し、焼結後、切刃稜線部に
Ｒ：０．０５のホーニング加工を施してＩＳＯ規格・Ｃ
ＮＭＧ１２０４０８および同ＳＥＥＮ１２０３ＡＦＴＮ
１のチップ形状をもったＷＣ基超硬合金製の超硬基体ａ
〜ｌをそれぞれ製造した。Next, the coated cemented carbide tip of the present invention will be specifically described with reference to examples. As raw material powder,
Average particle size: Medium-coarse WC powder having 5.5 μm;
8 μm fine WC powder, 2.3 μm Cr 3 C 2 powder,
1.2 μm VC powder, 1.5 μm TiC powder,
The same 1.3 μm TaC powder, the same 1.2 μm NbC powder, the same 1.0 μm (Ta, Nb) C [by mass ratio, Ta
C / NbC = 50/50] powder, 1.0 μm (T
i, W) A powder of C [TiC / WC = 70/30 by mass ratio] and a Co powder of 1.8 μm each were prepared, and these raw material powders were respectively blended into the blending composition shown in Table 1, After the wax was added, the mixture was mixed in a ball mill in acetone for 24 hours, dried under reduced pressure, and then pressed into a green compact having a predetermined shape at a pressure of 100 MPa.
In a vacuum atmosphere at a rate of 7 ° C./min.
The temperature was raised to a predetermined temperature in the range of 70 ° C., and after maintaining at this temperature for 1 hour, sintering was performed under furnace cooling conditions. ISO standard C
NMG120408 and SEEN1203AFTN
Carbide substrate a made of WC-based cemented carbide having a chip shape of 1
~ L were each manufactured.
【００１７】ついで、これらの超硬基体ａ〜ｌ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２
に例示される通常の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０．５Ｐａ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
１０ＰａのＡｒ雰囲気とし、この状態で超硬基体に−８
００ｖのバイアス電圧を印加して超硬基体表面を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
素ガスを導入して６Ｐａの反応雰囲気とすると共に、前
記超硬基体に印加するバイアス電圧を−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、もって前記超硬基体ａ〜ｌのそれぞれの
表面に、表２に示される目標組成（Ｘ値）および目標層
厚の（Ｔｉ，Ａｌ）Ｎ層を硬質被覆層の内側層として形
成し、さらに前記内側層の表面に、通常の化学蒸着装置
を用い、反応ガス組成を、容量％で、ＡｌＣｌ3：２
％、ＣＯ2：３％、Ｈ2Ｓ：０．３％、ＨＣｌ：１％、Ｈ
2：残り、からなる通常の反応ガス組成とし、かつ反応
雰囲気圧力も同じく通常の７ＫＰａとするが、反応雰囲
気温度は通常の反応雰囲気温度である１０００〜１０５
０℃に比して相対的に低い８２０℃とした中温化学蒸着
条件で、同じく表２に示される目標層厚のκ型結晶構造
のＡｌ2Ｏ3層を硬質被覆層の外側層として形成すること
により本発明被覆超硬チップ１〜１２をそれぞれ製造し
た。Next, these super-hard substrates a to l were ultrasonically cleaned in acetone and dried, respectively, as shown in FIG.
And a Ti-Al alloy having various component compositions as a cathode electrode (evaporation source), and the inside of the apparatus is evacuated to a vacuum of 0.5 Pa. After heating the inside of the apparatus to 500 ° C. with a heater, an Ar gas was introduced into the apparatus to form an Ar atmosphere of 10 Pa, and in this state, the superhard substrate was subjected to −8.
A bias voltage of 00 V is applied to clean the surface of the super hard substrate by Ar gas bombardment. Then, a nitrogen gas is introduced into the apparatus as a reaction gas to make a reaction atmosphere of 6 Pa, and the bias voltage applied to the super hard substrate is reduced. -200 v to generate an arc discharge between the cathode electrode and the anode electrode, thereby forming a target composition (X value) and a target layer shown in Table 2 on each surface of the cemented carbide substrates al. A thick (Ti, Al) N layer is formed as an inner layer of the hard coating layer, and the surface of the inner layer is further coated on a surface of the inner layer with an ordinary chemical vapor deposition apparatus using a reaction gas composition of AlCl 3 : 2 in volume%
%, CO 2 : 3%, H 2 S: 0.3%, HCl: 1%, H
2 : A normal reaction gas composition consisting of the remainder, and a reaction atmosphere pressure of the same normal 7 KPa, but a reaction atmosphere temperature of 1000 to 105 which is a normal reaction atmosphere temperature
Under a medium temperature chemical vapor deposition condition of 820 ° C. which is relatively lower than 0 ° C., an Al 2 O 3 layer having a κ-type crystal structure having a target layer thickness also shown in Table 2 is formed as an outer layer of the hard coating layer. Thereby, the coated superhard chips 1 to 12 of the present invention were manufactured.
【００１８】また、比較の目的で、表３に示される通り
上記の中温化学蒸着条件でのκ型結晶構造のＡｌ2Ｏ3層
の形成を行なわない以外は同一の条件で、硬質被覆層が
内側層の（Ｔｉ，Ａｌ）Ｎ層だけからなる比較被覆超硬
チップ１〜１２をそれぞれ製造した。For the purpose of comparison, as shown in Table 3, the hard coating layer was formed under the same conditions except that the Al 2 O 3 layer having the κ-type crystal structure was not formed under the above-mentioned medium temperature chemical vapor deposition conditions. Comparative coated carbide tips 1 to 12 each consisting of only the inner layer (Ti, Al) N were produced.
【００１９】なお、本発明被覆超硬チップ１〜１２およ
び比較被覆超硬チップ１〜１２の硬質被覆層について、
その構成層のそれぞれの厚さ方向中央部の組成をオージ
ェ分光分析装置を用いて測定すると共に、その厚さを、
走査型電子顕微鏡を用いて断面測定したところ、いずれ
も目標組成および目標層厚と実質的に同じ値を示した。The hard coating layers of the coated super hard tips 1 to 12 of the present invention and the comparative super hard tips 1 to 12 are as follows.
The composition of each central part in the thickness direction of the constituent layers is measured using an Auger spectroscopic analyzer, and the thickness is determined by:
When the cross-section was measured using a scanning electron microscope, all showed substantially the same values as the target composition and the target layer thickness.
【００２０】つぎに、上記本発明被覆超硬チップ１〜１
２および比較被覆超硬チップ１〜１２のＩＳＯ規格・Ｃ
ＮＭＧ１２０４０８のチップ形状のものについては、こ
れをいずれも工具鋼製バイトの先端部に固定治具にてネ
ジ止めした状態で、 被削材：ＪＩＳ・ＳＣＭ４４０の丸棒、 切削速度：３５０ｍ／ｍｉｎ．、 切り込み：２．０ｍｍ、 送り：０．２ｍｍ／ｒｅｖ．、 切削時間：１５分、 の条件での合金鋼の乾式高速連続旋削試験、 被削材：ＪＩＳ・ＦＣ３００の丸棒、 切削速度：３５０ｍ／ｍｉｎ．、 切り込み：２．０ｍｍ、 送り：０．３ｍｍ／ｒｅｖ．、 切削時間：１０分、 の条件での鋳鉄の乾式高速連続旋削試験を行ない、さら
に上記本発明被覆超硬チップ１〜１２および比較被覆超
硬チップ１〜１２のＩＳＯ規格・同ＳＥＥＮ１２０３Ａ
ＦＴＮ１のチップ形状をもったものについては、正面フ
ライス工具のカッター（直径：２００ｍｍ）の正面に１
個を固定治具でネジ止めした状態で、 被削材：ＪＩＳ・Ｓ５５Ｃの板材、 切削速度：３００ｍ／ｍｉｎ．、 切り込み：１．５ｍｍ、 送り：０．２ｍｍ／刃、 切削時間：１０分、 の条件での炭素鋼の乾式高速フライス切削試験をそれぞ
れ行い、いずれの乾式高速切削加工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２、３にそれぞ
れ示した。Next, the coated carbide tips 1 to 1 according to the present invention will be described.
2 and ISO standard for comparative coated carbide tips 1 to 12 ・ C
Regarding the tip shape of NMG120408, all of them were screwed to the tip of a tool steel tool with a fixing jig. Work material: JIS SCM440 round bar; Infeed: 2.0 mm Feed: 0.2 mm / rev. , Cutting time: 15 minutes, Dry high-speed continuous turning test of alloy steel under the following conditions: Work material: JIS FC300 round bar, Cutting speed: 350 m / min. Infeed: 2.0 mm Feed: 0.3 mm / rev. A dry high-speed continuous turning test of cast iron was performed under the following conditions: cutting time: 10 minutes, and the above-mentioned coated carbide tips 1 to 12 of the present invention and comparative coated carbide tips 1 to 12 were subjected to ISO standards and SEEN 1203A.
For the one with the FTN1 tip shape, one face is placed in front of the cutter (diameter: 200 mm) of the face milling tool.
Workpiece: JIS S55C plate, Cutting speed: 300 m / min. , Depth of cut: 1.5 mm, feed: 0.2 mm / tooth, cutting time: 10 minutes, dry high-speed milling test of carbon steel under the following conditions: flank surface of cutting edge in any dry high-speed cutting test The wear width was measured. The measurement results are shown in Tables 2 and 3, respectively.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】[0023]
【表３】 [Table 3]
【００２４】[0024]
【発明の効果】表１〜３に示される結果から、本発明被
覆超硬チップ１〜１２は、いずれもすぐれた高温強度お
よび高温硬さを有することから、鋼や鋳鉄の切削加工を
高い発熱を伴う高速で行っても、切刃に偏摩耗の発生な
く、すぐれた耐摩耗性を発揮するのに対して、硬質被覆
層が（Ｔｉ，Ａｌ）Ｎ層だけからなる、すなわち中温化
学蒸着条件でのκ型結晶構造のＡｌ2Ｏ3層の形成のない
比較被覆超硬チップ１〜１２においては、高温硬さ不足
が原因で摩耗の進行がきわめて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チップは、各種
の鋼や鋳鉄などの通常の条件での切削加工は勿論のこ
と、特に高速切削加工においてもすぐれた耐摩耗性を発
揮し、使用寿命の延命化を可能にするものであるから、
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。According to the results shown in Tables 1 to 3, all of the coated carbide tips 1 to 12 of the present invention have excellent high-temperature strength and high-temperature hardness. Even when the cutting is performed at a high speed, the cutting edge exhibits excellent wear resistance without uneven wear, whereas the hard coating layer is composed of only the (Ti, Al) N layer, that is, the medium temperature chemical vapor deposition condition. It is clear that in the comparative coated carbide tips 1 to 12 in which the Al 2 O 3 layer having the κ-type crystal structure was not formed, wear progressed extremely fast due to insufficient high-temperature hardness. As described above, the coated cemented carbide tip of the present invention exhibits excellent wear resistance not only in cutting under various conditions such as steel and cast iron, but also in high-speed cutting, and has a long service life. It is possible to extend the life of
The present invention can satisfactorily cope with labor saving, energy saving, and further cost reduction of the cutting process.
【図１】（ａ）は被覆超硬チップの概略斜視図で、
（ｂ）は同概略縦断面図である。FIG. 1A is a schematic perspective view of a coated carbide tip,
(B) is a schematic longitudinal sectional view of the same.
【図２】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. 2 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） Ｃ２３Ｃ 14/06 Ｃ２３Ｃ 14/06 Ａ 16/40 16/40 (72)発明者 中村 惠滋 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 Ｆターム(参考） 3C046 FF03 FF10 FF13 FF16 FF19 FF22 FF25 FF32 FF39 4K018 AD06 FA24 KA16 4K029 AA04 BA58 BB02 BC02 BD05 CA03 DD06 EA01 FA04 4K030 AA03 AA14 AA17 BA02 BA43 BB13 CA03 FA10 HA04 JA01──────────────────────────────────────────────────の Continued on the front page (51) Int.Cl. 7 Identification symbol FI Theme coat ゛ (Reference) C23C 14/06 C23C 14/06 A 16/40 16/40 (72) Inventor Keiji Nakamura Omiya City, Saitama Prefecture 1-297 Kitabukuro-cho Mitsubishi Materials Co., Ltd. Research Laboratory F-term (reference) FA10 HA04 JA01
Claims (2)
炭化タングステン基超硬合金基体の表面に、 （ａ）内側層として、０．５〜１０μｍの平均層厚を有
し、かつ物理蒸着法で形成された、組成式：（Ｔｉ1-X
ＡｌX）Ｎ（ただし、原子比で、Ｘは０．３〜０．７を
示す）を有するＴｉとＡｌの複合窒化物層、 （ｂ）外側層として、０．１〜５μｍの平均層厚を有
し、かつ中温化学蒸着法で形成された、κ型結晶構造の
酸化アルミニウム層、以上（ａ）および（ｂ）で構成さ
れた硬質被覆層を形成してなる、高速切削ですぐれた耐
摩耗性を発揮する表面被覆超硬合金製スローアウエイチ
ップ。1. A green compact having a composition of: 5 to 14% by mass of Co, 0.1 to 2% of chromium carbide, 0.1 to 2% of vanadium carbide, and 0.1% to 2% of tungsten carbide by mass%. (A) As an inner layer, a composition formula having an average layer thickness of 0.5 to 10 μm and formed by physical vapor deposition on the surface of a tungsten carbide-based cemented carbide substrate composed of a sintered body of : (Ti 1-X
(Al x ) N (where X represents 0.3 to 0.7 in atomic ratio), a composite nitride layer of Ti and Al, (b) an average layer thickness of 0.1 to 5 μm as an outer layer And an aluminum oxide layer having a κ-type crystal structure formed by a medium-temperature chemical vapor deposition method, and a hard coating layer composed of the above (a) and (b). Throwaway tips made of surface-coated cemented carbide that exhibit abrasion properties.
複合炭化物、およびＴｉとＷの複合炭化物のうちの１種
又は２種以上：０．５〜２５％、 炭化タングステン：残り、からなる配合組成を有する圧
粉体の焼結体で構成された炭化タングステン基超硬合金
基体の表面に、 （ａ）内側層として、０．５〜１０μｍの平均層厚を有
し、かつ物理蒸着法で形成された、組成式：（Ｔｉ1-X
ＡｌX）Ｎ（ただし、原子比で、Ｘは０．３〜０．７を
示す）を有するＴｉとＡｌの複合窒化物層、 （ｂ）外側層として、０．１〜５μｍの平均層厚を有
し、かつ中温化学蒸着法で形成された、κ型結晶構造の
酸化アルミニウム層、以上（ａ）および（ｂ）で構成さ
れた硬質被覆層を形成してなる、高速切削ですぐれた耐
摩耗性を発揮する表面被覆超硬合金製スローアウエイチ
ップ。2. Mass%, Co: 5 to 14%, Chromium carbide: 0.1 to 2%, Vanadium carbide: 0.1 to 2%, Titanium carbide, Niobium carbide, Tantalum carbide, Nb and Ta composite One or more of carbides and composite carbides of Ti and W: 0.5 to 25%, tungsten carbide: tungsten carbide composed of a sintered compact of a compact having a composition of the balance (A) An inner layer having an average layer thickness of 0.5 to 10 μm and formed by a physical vapor deposition method and having a composition formula of (Ti 1-X
(Al x ) N (where X represents 0.3 to 0.7 in atomic ratio), a composite nitride layer of Ti and Al, (b) an average layer thickness of 0.1 to 5 μm as an outer layer And an aluminum oxide layer having a κ-type crystal structure formed by a medium-temperature chemical vapor deposition method, and a hard coating layer composed of the above (a) and (b). Throwaway tips made of surface-coated cemented carbide that exhibit abrasion properties.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000397081A JP2002200502A (en) | 2000-12-27 | 2000-12-27 | Surface coated cemented carbide throw away tip exerting excellent wear resistance by high speed cutting |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000397081A JP2002200502A (en) | 2000-12-27 | 2000-12-27 | Surface coated cemented carbide throw away tip exerting excellent wear resistance by high speed cutting |
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| Publication Number | Publication Date |
|---|---|
| JP2002200502A true JP2002200502A (en) | 2002-07-16 |
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ID=18862264
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104480337A (en) * | 2014-12-15 | 2015-04-01 | 技锋精密刀具（马鞍山）有限公司 | Preparation method of material for hard alloy slitting tool |
-
2000
- 2000-12-27 JP JP2000397081A patent/JP2002200502A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104480337A (en) * | 2014-12-15 | 2015-04-01 | 技锋精密刀具（马鞍山）有限公司 | Preparation method of material for hard alloy slitting tool |
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