JPH07122138B2 - Surface coated cemented carbide member - Google Patents
Surface coated cemented carbide memberInfo
- Publication number
- JPH07122138B2 JPH07122138B2 JP10592587A JP10592587A JPH07122138B2 JP H07122138 B2 JPH07122138 B2 JP H07122138B2 JP 10592587 A JP10592587 A JP 10592587A JP 10592587 A JP10592587 A JP 10592587A JP H07122138 B2 JPH07122138 B2 JP H07122138B2
- Authority
- JP
- Japan
- Prior art keywords
- layer
- cemented carbide
- balance
- carbonitrides
- composition
- 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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- Chemical Vapour Deposition (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 この発明は、すぐれた耐摩耗性および耐塑性変形性を有
し、かつ靱性に富んだ、被覆層の密着性の強い、すぐれ
た切削性を示す表面被覆超硬合金部材に関するものであ
る。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention has excellent wear resistance and plastic deformation resistance, is rich in toughness, has a strong coating layer adhesion, and has excellent machinability. The present invention relates to a surface-coated cemented carbide member having
従来、例えば炭化タングステン（以下WCで示す）基超硬
合金基体の表面に、周期律表4a,5aおよび6a族の金属の
炭化物（但しWCを除く）、窒化物、炭窒化物、炭酸化
物、および炭酸窒化物、並びに酸化アルミニウム、さら
にこれらの２種以上の固溶体からなる群のうちの１種の
単層または２種以上の多重層からなる被覆層を形成した
表面被覆超硬合金部材は公知であり、この公知の表面被
覆超硬合金部材の靱性をさらに改良するために、超硬合
金基体の表面にWC−Coからなる中間軟化層、さらにその
上にNaCl型結晶構造物−Coからなる表面硬質層を設けて
超硬合金基体を改質した上で最終の被覆層を形成するこ
とにより、被覆層の密着性を改善する方法が試みられ
（特開昭55−134107号公報）、すぐれた効果をあげてい
る。Conventionally, for example, on the surface of a tungsten carbide (hereinafter referred to as WC) -based cemented carbide substrate, carbides of metals of groups 4a, 5a and 6a of the periodic table (excluding WC), nitrides, carbonitrides, carbonates, A surface-coated cemented carbide member having a coating layer formed of a single layer or two or more multi-layers selected from the group consisting of a solid solution of two or more kinds of these, a carbonitride, and an aluminum oxide is known. In order to further improve the toughness of this known surface-coated cemented carbide member, an intermediate softening layer made of WC-Co is formed on the surface of the cemented carbide substrate, and further a NaCl-type crystal structure-Co is formed thereon. A method of improving the adhesion of the coating layer has been attempted by forming a final coating layer after modifying the cemented carbide substrate by providing a hard surface layer (JP-A-55-134107), which is excellent. The effect is good.
しかしながら、上記特開昭55−134107号公報記載の方法
によつても得られる被覆工具材は連続切削では良好な特
性を示すものの、断続切削では被覆層の剥離が起るとい
う問題点があつた。However, although the coated tool material obtained by the method described in JP-A-55-134107 has good characteristics in continuous cutting, there is a problem that peeling of the coating layer occurs in intermittent cutting. .
そこで、本発明者等は、上記従来の表面被覆超硬合金部
材のもつ問題点を解決して、断続切削時においても耐塑
性変形性および靱性にすぐれ、かつ被覆層の密着性が高
く剥離の起らない表面被覆超硬合金部材を得べく研究を
行つた結果、 上記超硬合金基体の表面と被覆層との間に、超硬合金基
体の内部よりも軟らかく、靱性に富んだ中間軟化層と上
記中間軟化層よりも硬質の表面準硬質層を形成すれば、
被覆層と超硬合金基体との変形に対する追従性が良好と
なり剥離の発生が抑えられ、さらに被覆層よりのクラツ
クの伝播が抑制でき、靱性の大幅な向上がはかられ、断
続切削に対する良好な特性が得られるという知見を得た
のである。Therefore, the present inventors have solved the problems of the above conventional surface-coated cemented carbide members, excellent plastic deformation resistance and toughness even during interrupted cutting, and high adhesiveness of the coating layer As a result of conducting research to obtain a surface-coated cemented carbide member that does not occur, an intermediate softened layer between the surface of the cemented carbide substrate and the coating layer, which is softer than the inside of the cemented carbide substrate and rich in toughness. And by forming a surface semi-hard layer harder than the intermediate softening layer,
The followability to the deformation of the coating layer and the cemented carbide substrate is good, the occurrence of delamination is suppressed, the propagation of cracks from the coating layer can be suppressed, the toughness is greatly improved, and it is good for intermittent cutting. We have obtained the knowledge that the characteristics can be obtained.
この発明は、かかる知見にもとづいてなされたものであ
つて、 超硬合金基体の表面に形成した層厚:2〜50μｍの中間軟
化層と、該中間軟化層の上に形成した層厚:0.1〜30μｍ
の表面準硬質層と、該表面準硬質層の上に形成した層
厚:1〜20μｍの被覆層とからなる表面被覆超硬合金部材
であつて、 該超硬合金基体の内部を、 Co:5〜30％容量％（以下、成分組成についての％は容量
％）、WC:残部からなる組成、または、周期律表の4a、5
aおよび6a族の金属の炭化物（但しWCを除く）、窒化物
および炭窒化物のうち１種または２種以上からなるNaCl
型結晶構造物:5〜30％、Co:5〜30％、WC:残部からなる
組成で構成し、 該中間軟化層は、 Co:15〜30％、WC:残部からなる組成、または、周期律表
の4a、5aおよび6a族の金属の炭化物（但しWCを除く）、
窒化物および炭窒化物のうち１種または２種以上からな
るNaCl型結晶構造物:5〜30％、Co:5〜30％、WC:残部か
らなる組成から構成され、 該表面準硬質層は、 Co:3〜15％、WC:残部からなる組成、または、周期律表
の4a、5aおよび6a族の金属の炭化物（但しWCを除く）、
窒化物および炭窒化物のうち１種または２種以上からな
るNaCl型結晶構造物:5〜30％、Co:3〜15％、WC:残部か
らなる組成から構成され、 該被覆層は、 周期律表の4a、5aおよび6a族の金属の炭化物（但しWCを
除く）、窒化物および炭窒化物、炭酸化物および炭酸窒
化物、並びに酸化アルミニウム、さらにこれらの２種以
上の固溶体からなる群のうち１種の単層または２種以上
の多層からなる組成から構成され、 該表面準硬化層の硬さが、該中間軟化層の硬さよりもビ
ツカース硬さで５〜125％硬く、該中間軟化層は、該超
硬合金基体内部に比べて、ビツカース硬さで20〜60％軟
化している組織を有する表面被覆超硬合金部材に特徴を
有するものである。The present invention has been made on the basis of the above finding, wherein the layer thickness formed on the surface of the cemented carbide substrate: 2 to 50 μm, the intermediate softening layer, and the layer thickness formed on the intermediate softening layer: 0.1 ~ 30 μm
A surface-coated cemented carbide member comprising a surface quasi-hard layer of, and a coating layer having a layer thickness of 1 to 20 μm formed on the surface quasi-hard layer, wherein the inside of the cemented carbide substrate is Co: 5 to 30% by volume (hereinafter,% of the component composition is% by volume), WC: composition consisting of the balance, or 4a, 5 of the periodic table
NaCl consisting of one or more of carbides (excluding WC), nitrides and carbonitrides of a and 6a group metals
Type crystal structure: 5 to 30%, Co: 5 to 30%, WC: WC: balance composition, the intermediate softening layer, Co: 15 to 30%, WC: balance composition, or period Carbides of metals of groups 4a, 5a and 6a of the table (excluding WC),
An NaCl type crystal structure composed of one or more kinds of nitrides and carbonitrides: 5 to 30%, Co: 5 to 30%, WC: a composition consisting of the balance, and the surface semi-hard layer is , Co: 3-15%, WC: composition consisting of the balance, or carbides of metals of groups 4a, 5a and 6a of the periodic table (excluding WC),
A NaCl type crystal structure consisting of one or more of nitrides and carbonitrides: 5 to 30%, Co: 3 to 15%, WC: the composition of the balance, and the coating layer has a periodic structure. Of the group consisting of carbides (except WC), nitrides and carbonitrides, carbonates and carbonitrides of the metals of groups 4a, 5a and 6a of the table, as well as aluminum oxide and solid solutions of two or more of these Among them, the composition is composed of one kind of single layer or two or more kinds of multilayers, and the surface semi-cured layer has a hardness of 5 to 125% in Vickers hardness than the hardness of the intermediate softened layer. The layer is characteristic of a surface-coated cemented carbide member having a structure in which it is 20-60% softened in Vickers hardness as compared with the inside of the cemented carbide substrate.
つぎに、この発明の表面被覆超硬合金部材における被覆
層、表面準硬質層、中間軟化層および超硬合金基体内部
の組成および硬さの限定理由について述べるが、上記被
覆層および超硬合金基体内部の組成は、公知のものであ
るから詳述せず、上記表面準硬質層および中間軟化層の
組成および硬さについて詳述する。Next, the reasons for limiting the composition and hardness of the coating layer, the surface semi-hard layer, the intermediate softening layer and the inside of the cemented carbide substrate in the surface-coated cemented carbide member of the present invention will be described. The internal composition is well known and will not be described in detail. The composition and hardness of the surface semi-hard layer and the intermediate softening layer will be described in detail.
（ａ）表面準硬質層 被覆層の剥離は、切削時の塑性変形に対する被覆層と超
硬合金基体との靱性の不一致の程度の大きさによるとこ
ろが大きい。したがつて、この発明においては、被覆層
と中間軟化層との間に、中間軟化層よりも硬い表面準硬
質層を形成し、被覆層と中間軟化層との硬さの違いを緩
和し、被覆層の強度不足を補うとともに変形に対する追
従性を改善し被覆層の密着性の向上をはかつたものであ
る。(A) Surface semi-hard layer The peeling of the coating layer is largely due to the extent of the degree of inconsistency in the toughness between the coating layer and the cemented carbide substrate with respect to plastic deformation during cutting. Therefore, in the present invention, between the coating layer and the intermediate softening layer, a surface semi-hard layer harder than the intermediate softening layer is formed, and the difference in hardness between the coating layer and the intermediate softening layer is relaxed, The strength of the coating layer is compensated, the followability to deformation is improved, and the adhesion of the coating layer is improved.
この表面準硬質層の組成は、Co:3〜15％、WC:残部、ま
たはCo:3〜15％、周期律表の4a、5aおよび6a族の金属の
炭化物（但しWCを除く）、窒化物および炭窒化物のうち
１種または２種以上からなるNaCl型結晶構造物（以下、
単にNaCl型化合物という）:5〜30％、WC:残部のいずれ
かから成り、Co:3％未満では所望の靱性が得られず、15
％を越えて含有させると所望の硬さが得られず、耐摩耗
性の不足につながる。NaCl型化合物についても、５％未
満では耐摩耗性が不足し、30％を越えると靱性が不足す
る。なお、WCおよびNaCl型化合物の粒度については、一
般に中間軟化層中のWCおよびNaCl型化合物の粒度よりや
や細い方が好ましい。The composition of the surface semi-hard layer is Co: 3 to 15%, WC: balance, or Co: 3 to 15%, carbides of metals of groups 4a, 5a and 6a of the periodic table (excluding WC), nitriding Crystals and carbonitrides, which are composed of one or more kinds of NaCl type crystal structures (hereinafter,
Simply referred to as NaCl-type compound): 5-30%, WC: any of the balance, Co: less than 3%, the desired toughness cannot be obtained.
If it is contained in excess of%, the desired hardness cannot be obtained, leading to insufficient wear resistance. Also with respect to the NaCl type compound, if it is less than 5%, the wear resistance is insufficient, and if it exceeds 30%, the toughness is insufficient. Regarding the particle size of the WC and NaCl type compounds, it is generally preferable that it is slightly smaller than the particle size of the WC and NaCl type compounds in the intermediate softening layer.
表面基硬化質の硬さは、中間軟化層の硬さよりビツカー
ス硬さで５〜125％硬いことが必要であり、５％未満で
は所望の改善効果が得られず、一方125％を越えて硬化
させると、靱性低下が著しい。The hardness of the surface-based curable material needs to be 5 to 125% harder than the hardness of the intermediate softening layer in terms of Vickers hardness. If it is less than 5%, the desired improvement effect cannot be obtained, while the hardness exceeds 125%. If so, the toughness is significantly reduced.
また、表面準硬質層の層圧が0.1μｍ未満では同様に所
望の改善効果がなく、30μｍを越えると靱性の低下をき
たすという理由により、その層厚を0.1〜30μｍと定め
たのである。Similarly, if the layer pressure of the surface semi-hard layer is less than 0.1 μm, the desired improving effect is not obtained, and if it exceeds 30 μm, the toughness is deteriorated. Therefore, the layer thickness is set to 0.1 to 30 μm.
（ｂ）中間軟化層 表面被覆超硬合金工具の欠損は、通常被覆層よりの超硬
合金基体内部へのクラツク伝播により生じると考えられ
ており、したがつて、この発明では、上記表面準硬質層
と超硬合金基体表面部との間に、層厚:2〜50μｍで、超
硬合金基体内部よりビツカース硬さで20〜60％軟化した
靱性に富んだ軟化層を形成することによつて、硬質被覆
層よりのクラツクの伝播の抑制すると共に、強度および
靱性の向上をはかつたのである。中間軟化層の硬さが、
超硬合金基体内部に比してビツカース硬さで20％未満の
軟化では、所望の靱性改善効果を確保することができ
ず、一方60％を越えて軟化させると、耐塑性変形性およ
び被覆の耐剥離性の低下が著しいことから、中間軟化層
の硬さを基体内部硬さよりビツカース硬さで20〜60％軟
化させた硬さとしたのである。(B) Intermediate softening layer It is considered that the defect of the surface-coated cemented carbide tool is usually caused by crack propagation from the coating layer into the cemented carbide substrate. Therefore, in the present invention, the surface quasi-hardened surface is hard. By forming a softened layer rich in toughness between the layer and the surface of the cemented carbide substrate with a layer thickness of 2 to 50 μm, which is 20 to 60% softened by Vickers hardness from the inside of the cemented carbide substrate. In addition to suppressing crack propagation from the hard coating layer, the strength and toughness are improved. The hardness of the intermediate softening layer is
A softening of less than 20% in Vickers hardness compared to the inside of the cemented carbide substrate cannot ensure the desired toughness improving effect, while softening over 60% results in plastic deformation resistance and coating Since the peeling resistance is remarkably lowered, the hardness of the intermediate softening layer is set to be a hardness that is 20 to 60% softer than the internal hardness of the substrate in terms of Vickers hardness.
さらに、層圧が２μｍ未満では、同様に所望の靱性改善
効果が得られず、一方50μｍを越えた層厚にすると、著
しい耐塑性変形性の低下をきたすことから、中間軟化層
の層厚を２〜50μｍと定めたのである。Further, if the layer pressure is less than 2 μm, the desired toughness-improving effect cannot be similarly obtained. On the other hand, if the layer thickness exceeds 50 μm, the plastic deformation resistance is remarkably reduced, so the layer thickness of the intermediate softening layer is reduced. It was set to 2 to 50 μm.
中間軟化層は、Co:15〜30％、WC:残部、または、Co:15
〜30％、NaCl型化合物:5〜30％、WC:残部からなる組成
で構成され、その限定理由も表面準硬質層で述べた内容
と同一である。但し、WCおよびNaCl型化合物の粒度は、
表面準硬質層のWCおよびNaCl型化合物の粒度より、やや
粗い方が好ましい。The intermediate softening layer is Co: 15-30%, WC: balance, or Co: 15
.About.30%, NaCl type compound: 5 to 30%, WC: balance, and the reason for limitation is the same as that described in the surface semi-hard layer. However, the particle size of WC and NaCl type compound is
It is preferable that the surface semi-hard layer is a little coarser than the particle size of the WC and NaCl type compounds.
なお、被覆層の層厚に関しては、その層厚が１μｍ未満
では所望の耐摩耗性改善効果が確保できず、一方20μｍ
を越えた層厚にすると、靱性低下が著しいことから１〜
20μｍと定めた。この被覆層は、通常の化学蒸着法、イ
オンプレーテイング法およびスパツタリング法などの被
覆層形成手段によつて形成することができる。Regarding the layer thickness of the coating layer, if the layer thickness is less than 1 μm, the desired effect of improving wear resistance cannot be ensured, while the thickness of 20 μm
If the layer thickness exceeds 1.0, the toughness is significantly reduced.
It was set to 20 μm. This coating layer can be formed by a conventional coating layer forming means such as a chemical vapor deposition method, an ion plating method and a sputtering method.
つぎに、この発明を実施例にもとづいて具体的に説明す
る。Next, the present invention will be specifically described based on Examples.
超硬合金基体の内部組成として、第１表に示すような最
終成分組成となるように市販の原料粉末を配合し、ボー
ルミルにて48時間湿式混合し、乾燥し、プレスすること
によつて圧粉体を成形し、ついで、圧粉体の表面に、別
途予め用意した第１表の中間軟化層形成のための所定の
配合粉末混合スラリーをN2ガス雰囲気中で一様に噴霧し
て減圧下で乾燥し、引き続いて表面準硬質層形成のため
の第１表に示した配合粉混合スラリーを同様に所定の厚
みになるようにN2ガス雰囲気中で一様に噴霧し、減圧下
で乾燥し、ついで温度:1400℃に１時間保持して焼結す
ることによつて、表面準硬質層および中間軟化層を有す
るSNU432型スローアウエイチツプを製造し、表面準硬質
層および中間軟化層の層厚およびビツカース硬さを測定
し、第１表に示した。As the internal composition of the cemented carbide substrate, commercially available raw material powders are blended so that the final composition shown in Table 1 is obtained, and the mixture is wet mixed in a ball mill for 48 hours, dried, and pressed. The powder is molded, and then a predetermined blended powder mixed slurry for forming the intermediate softening layer shown in Table 1 is sprayed uniformly on the surface of the green compact in a N 2 gas atmosphere to reduce the pressure. And then sprayed uniformly with the mixed powder mixture slurry shown in Table 1 for forming the surface semi-hard layer in a N 2 gas atmosphere to a predetermined thickness, and then reducing the pressure. A SNU432 type throwaway chip having a surface quasi-hard layer and an intermediate softening layer was produced by drying and then sintering at a temperature of 1400 ° C. for 1 hour to obtain a surface quasi-hard layer and an intermediate softening layer. The layer thickness and Vickers hardness were measured and are shown in Table 1.
上記SNU432型スローアウエイチツプの表面に、0.05mmの
プレホーニングを施し、化学蒸着溶処理炉内に装入し、
大気圧下でTiCl4:4％、CH4:4％およびH2:92％（容量
％）からなるガスを導入しながら、温度:1050℃に５時
間保持することによつて、層厚:5μｍのTic層を被覆
し、つづいてAlCl3:2％、CO2:6％およびH2:92％（容量
％）からなるガスを導入しながら、温度:1000℃で２時
間保持することによつて層厚:1μｍのAl2O3層を被覆
し、計６μｍの被覆層を形成し、本発明スローアウエイ
チツプ を製造した。On the surface of the SNU432 type throwaway chip, 0.05 mm pre-honing was applied, and it was placed in the chemical vapor deposition furnace.
By introducing a gas consisting of TiCl 4 : 4%, CH 4 : 4% and H 2 : 92% (volume%) under atmospheric pressure and maintaining the temperature at 1050 ° C for 5 hours, the layer thickness: A 5 μm thick Tic layer is coated, and then a gas consisting of AlCl 3 : 2%, CO 2 : 6% and H 2 : 92% (volume%) is introduced, and the temperature is kept at 1000 ° C. for 2 hours. Therefore, the throwaway chip of the present invention is formed by coating an Al 2 O 3 layer having a thickness of 1 μm to form a coating layer having a total thickness of 6 μm. Was manufactured.
上記本発明スローアウエイチツプについて、 （１） 被削材:SNCM439（HB:320） 切削速度:150m/mim 送り:0.6mm/rev. 切込み:3mm の条件で連続切削試験を行ない、逃げ面摩耗およびクレ
ータ摩耗を測定した。Regarding the above-mentioned throwaway tip of the present invention, (1) Work material: SNCM439 (H B : 320) Cutting speed: 150 m / mim Feed: 0.6 mm / rev. Depth of cut: 3 mm, continuous cutting test was performed, flank wear And crater wear was measured.
（２） 被削材:SNCM439（HB:270）溝付き丸棒 切削速度:120m/mim 送り:0.4mm/rev. 切込み:3mm の条件で連続切削試験を行ない、切刃が欠損するまでの
時間を測定した。(2) Work material: SNCM439 (H B : 270) Round bar with groove Cutting speed: 120m / mim Feed: 0.4mm / rev. Depth of cut: 3mm Perform continuous cutting test until the cutting edge is broken. The time was measured.
上記（１）および（２）の切削試験の結果についても第
１表に示した。The results of the cutting tests (1) and (2) are also shown in Table 1.
ついで、従来例として、上記特開昭55−134107号公報に
示された、WCを含有しない表面硬化層を有する従来のス
ローアウエイチツプを用いて、上記（１）および（２）
の条件と同一の条件で切削試験をした。その結果も第２
表に示した。Then, as a conventional example, the conventional slow-away chip having a surface-hardened layer containing no WC, which is disclosed in JP-A-55-134107, is used, and the above-mentioned (1) and (2) are used.
A cutting test was performed under the same conditions as those of. The result is also the second
Shown in the table.
上記本発明のスローアウエイチツプを用いて切削試験を
した結果（第１表）と従来のスローアウエイチツプを用
いて切削試験をした結果（第２表）とを対比してみる
と、連続切削試験においては両者とも同じ効果を奏する
が、断続切削試験に対しては、本発明のスローアウエイ
チツプの方がはるかにすぐれていることが明らかであ
る。したがつて、この発明を切削工具として用いて、表
面に凹凸があるような被切削しても、従来の切削工具よ
り欠損時間が長く、断続切削に対してすぐれた効果を奏
するものである。Continuing cutting test is performed by comparing the result of cutting test using the throwaway chip of the present invention (Table 1) with the result of cutting test using conventional throwaway chip (Table 2). Both of them have the same effect, but it is apparent that the throwaway tip of the present invention is far superior to the intermittent cutting test. Therefore, even when the present invention is used as a cutting tool and is cut with an uneven surface, the defect time is longer than that of a conventional cutting tool and an excellent effect is obtained for intermittent cutting.
フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２３Ｃ 16/34 16/36 16/40 Continuation of front page (51) Int.Cl. 6 Identification code Office reference number FI technical display location C23C 16/34 16/36 16/40
Claims (1)
μｍの中間軟化層と、該中間軟化層の上に形成した層
厚:0.1〜30μｍの表面準硬質層と、該表面基準硬質層の
上に形成した層厚:1〜20μｍの被覆層からなる表面被覆
超硬合金部材であつて、 該超硬合金基体の内部を、 Co:5〜30％、WC:残部からなる組成、または、 周期律表の4a、5aおよび6a族の金属の炭化物（但しWCは
除く）、窒化物および炭窒化物のうち１種または２種以
上からなるNaCl型結晶構造物:5〜30％、Co:5〜30％、W
C:残部からなる組成から構成し、 該中間軟化層は、 Co:15〜30％、WC:残部からなる組成または、 周期律表の4a、5aおよび6a族の金属の炭化物（但しWCを
除く）、窒化物および炭窒化物のうち１種または２種以
上からなるNaCl型結晶構造物:5〜30％、Co:15〜30％、W
C:残部からなる組成から構成され、 該表面準硬質層は、 Co:3〜15％、WC:残部からなる組成または、 周期律表の4a、taおよび6a族の金属の炭化物（但しWCは
除く）、窒化物および炭窒化物のうち１種または２種以
上からなるNaCl型結晶構造物:5〜30％、Co:3〜15％、W
C:、残部からなる組成から構成され、 該被覆層は、 周期律表の4a、5aおよび6a族の金属の炭化物（但しWCを
除く）、窒化物および炭窒化物、炭酸化物および炭酸窒
化物、並びに酸化アルミニウム、さらにこれらの２種以
上の固溶体からなる群のうちの１種の単層または２種以
上の多層からなる組成から構成され（以上、％は容量
％）、 該表面準硬化層の硬さが、該中間軟化層の硬さよりもビ
ツカース硬さで５〜125％硬く、該中間軟化層は、該超
硬合金基体内に比べて、ビツカース硬さで20〜60％軟化
している組織を有することを特徴とする表面被覆超硬合
金部材。1. A layer thickness formed on the surface of a cemented carbide substrate: 2 to 50
consisting of an intermediate softening layer of μm, a layer thickness formed on the intermediate softening layer: 0.1 to 30 μm, a surface semi-hard layer, and a layer thickness formed on the surface reference hard layer: 1 to 20 μm A surface-coated cemented carbide member, wherein the inside of the cemented carbide substrate is composed of Co: 5 to 30%, WC: balance, or a carbide of a metal of group 4a, 5a and 6a of the periodic table ( (Except WC), NaCl-type crystal structure consisting of one or more of nitrides and carbonitrides: 5-30%, Co: 5-30%, W
C: a composition comprising the balance, the intermediate softening layer comprises Co: 15 to 30%, WC: a composition comprising the balance, or a metal carbide of a group 4a, 5a and 6a of the periodic table (excluding WC) ), A NaCl-type crystal structure composed of one or more of nitrides and carbonitrides: 5 to 30%, Co: 15 to 30%, W
C: a composition consisting of the balance, the surface quasi-hard layer has Co: 3 to 15%, WC: a composition consisting of the balance, or a metal carbide of a group 4a, ta and 6a of the periodic table (however, WC is (Excluding), NaCl-type crystal structure consisting of one or more of nitrides and carbonitrides: 5 to 30%, Co: 3 to 15%, W
C :, the composition consisting of the balance, and the coating layer is made of metal carbides (excluding WC), nitrides and carbonitrides, carbonates and carbonitrides of metals of groups 4a, 5a and 6a of the periodic table. And aluminum oxide, and a composition consisting of one single layer or two or more multilayers of the group consisting of two or more solid solutions of these (the above,% is% by volume). Of the Vickers hardness is 5 to 125% harder than the hardness of the intermediate softening layer, and the intermediate softening layer is 20 to 60% softer in Vickers hardness than in the cemented carbide substrate. A surface-coated cemented carbide member having a textured structure.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10592587A JPH07122138B2 (en) | 1987-04-28 | 1987-04-28 | Surface coated cemented carbide member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10592587A JPH07122138B2 (en) | 1987-04-28 | 1987-04-28 | Surface coated cemented carbide member |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63274771A JPS63274771A (en) | 1988-11-11 |
| JPH07122138B2 true JPH07122138B2 (en) | 1995-12-25 |
Family
ID=14420435
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10592587A Expired - Lifetime JPH07122138B2 (en) | 1987-04-28 | 1987-04-28 | Surface coated cemented carbide member |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07122138B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5204167A (en) * | 1989-02-23 | 1993-04-20 | Toshiba Tungaloy Co., Ltd. | Diamond-coated sintered body excellent in adhesion and process for preparing the same |
| JP3677406B2 (en) * | 1999-01-29 | 2005-08-03 | 京セラ株式会社 | Coated cemented carbide cutting tool |
| JP7021493B2 (en) * | 2017-09-29 | 2022-02-17 | 三菱マテリアル株式会社 | Composite sintered body |
-
1987
- 1987-04-28 JP JP10592587A patent/JPH07122138B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63274771A (en) | 1988-11-11 |
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