JPH10244406A - Throwaway type cutting tip made of surface-covering cermet with its hard covering layer having excellent breakage resistance - Google Patents
Throwaway type cutting tip made of surface-covering cermet with its hard covering layer having excellent breakage resistanceInfo
- Publication number
- JPH10244406A JPH10244406A JP5017097A JP5017097A JPH10244406A JP H10244406 A JPH10244406 A JP H10244406A JP 5017097 A JP5017097 A JP 5017097A JP 5017097 A JP5017097 A JP 5017097A JP H10244406 A JPH10244406 A JP H10244406A
- Authority
- JP
- Japan
- Prior art keywords
- hardness
- cermet
- cutting
- cutting tip
- 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.)
- Granted
Links
Landscapes
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
Description
【0001】[0001]
【発明の属する技術分野】この発明は、炭窒化チタン系
サーメットで構成された基体(以下、サーメット基体と
云う)の表面部に形成された表面硬化層における逃げ面
とすくい面が交わる切刃稜線部(以下、単に切刃稜線部
と云う)における硬さを、逃げ面およびすくい面におけ
る硬さに比して相対的に高くし、これによって前記基体
表面に物理蒸着(以下、PVDで示す)および/または
化学蒸着(以下、CVDで示す)される硬質被覆層にす
ぐれた耐欠損性を付与せしめ、もって耐欠損性が要求さ
れる、例えば鋼などの高速断続切削に用いた場合にも切
刃に欠けやチッピング(微小欠け)などの発生なく、す
くれた切削性能を長期に亘って発揮するようにした表面
被覆サーメット製スローアウエイ型切削チップ(以下、
単に被覆切削チップと云う)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 edge ridge line in which a flank and a rake face of a hardened surface layer formed on the surface of a substrate made of a titanium carbonitride-based cermet (hereinafter referred to as a cermet substrate). The hardness at the portion (hereinafter simply referred to as the cutting edge ridge portion) is made relatively higher than the hardness at the flank and rake face, whereby physical vapor deposition (hereinafter, referred to as PVD) is performed on the substrate surface. And / or imparts excellent fracture resistance to a hard coating layer to be subjected to chemical vapor deposition (hereinafter, referred to as CVD), so that it can be cut even when used for high-speed interrupted cutting of steel or the like, which requires fracture resistance. A surface-coated cermet throw-away type cutting tip (hereinafter, referred to as "the cutting edge") that can exhibit long-lasting cutting performance without causing chipping or chipping (small chipping) of the blade.
Simply referred to as a coated cutting tip).
【0002】[0002]
【従来の技術】従来、一般に例えば特開平4−3415
80号公報などに記載されるように、結合相形成成分と
してCoおよび/またはNiを5〜14重量%含有し、
ビッカース硬さ(以下、Hvで示す)で、Hv:140
0〜1800を示す内部硬さに対して、切刃の逃げ面、
切刃稜線部、およびすくい面にかけての表面部に、最高
表面硬さがHv:2100〜2500の均一な硬さ分布
をもった表面硬化層を形成したサーメット基体の表面
に、硬質被覆層を2〜20μmの平均層厚でPVD法お
よび/またはCVD法を用いて蒸着してなる被覆切削チ
ップが知られており、また、これが例えば鋼などの連続
切削や断続切削に用いられていることも知られている。
さらに、上記従来被覆切削チップを構成するサーメット
基体が、以下の条件、すなわち、(a)焼結温度への昇
温速度:1〜3℃/sec、(b)室温から1100〜
1300℃への昇温雰囲気:0.1torr以下の真
空、(c)1100〜1300℃から焼結温度である1
480〜1560℃への昇温雰囲気:5〜100tor
rの窒素雰囲気、(d)上記焼結温度での保持時間およ
び雰囲気:60〜90分および5〜100torrの窒
素雰囲気、(e)冷却:0.1torr以下の真空雰囲
気で炉冷、以上(a)〜(e)の条件を満足する条件
で、所定の配合組成を有する圧粉体を焼結することによ
って製造されることも知られている。2. Description of the Related Art Conventionally, for example, Japanese Patent Application Laid-Open No.
No. 80, etc., containing 5 to 14% by weight of Co and / or Ni as a binder phase forming component;
Vickers hardness (hereinafter referred to as Hv), Hv: 140
For the internal hardness of 0 to 1800, the flank of the cutting edge,
A hard coating layer was formed on the surface of a cermet substrate having a surface hardened layer having a uniform hardness distribution with a maximum surface hardness of Hv: 2100 to 2500 on the cutting edge ridge portion and the rake face. 2. Description of the Related Art Coated cutting tips formed by vapor deposition using a PVD method and / or a CVD method with an average layer thickness of 2020 μm are known, and it is also known that they are used for continuous cutting and interrupted cutting of, for example, steel. Have been.
Further, the cermet substrate constituting the above-mentioned conventional coated cutting tip is subjected to the following conditions: (a) a temperature rising rate to a sintering temperature: 1 to 3 ° C./sec;
Atmosphere of temperature rise to 1300 ° C .: vacuum of 0.1 torr or less, (c) sintering temperature from 1100 ° C. to 1300 ° C.
Temperature rising atmosphere to 480 to 1560 ° C: 5 to 100 torr
(d) Holding time and atmosphere at the above sintering temperature: 60 to 90 minutes and 5 to 100 torr nitrogen atmosphere; (e) Cooling: furnace cooling in a vacuum atmosphere of 0.1 torr or less; It is also known that the green compact is manufactured by sintering a green compact having a predetermined composition under the conditions satisfying the conditions (1) to (e).
【0003】[0003]
【発明が解決しようとする課題】一方、近年の切削装置
の高性能化はめざましく、かつ省力化に対する要求も強
く、これに伴い切削加工は高速化の傾向にあるが、上記
のサーメット基体の表面部に形成された表面硬化層の硬
さ分布に変化のない従来被覆切削チップにおいては、こ
れを例えば鋼の高速断続切削に用いた場合に硬質被覆層
の耐欠損性不足が原因で、切刃に欠けやチッピングなど
が発生し易く、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 performance of cutting devices has been remarkably improved, and there has been a strong demand for labor saving. Accordingly, the cutting process has tended to be accelerated. In conventional coated cutting tips where the hardness distribution of the surface hardened layer formed in the part does not change, when this is used for high-speed interrupted cutting of steel, for example, the cutting edge is insufficient due to insufficient fracture resistance of the hard coated layer. At present, chipping, chipping, and the like are liable to occur, and the service life is relatively short.
【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、上記のサーメット基体の表面部
に表面硬化層を形成した従来被覆切削チップに着目し、
これを構成する硬質被覆層の耐欠損性向上をはかるべく
研究を行った結果、サーメット基体の焼結に際して、結
合相形成成分であるCoおよび/またはNiの含有量を
7〜17重量%と特定した上で、上記の焼結条件である
(a)〜(e)の条件のうちの(e)条件の冷却雰囲気
を1〜5torrの窒素雰囲気とした条件で焼結を行な
うと、焼結後のサーメット基体の表面部には、切刃稜線
部が従来サーメット基体の表面硬化層に比して相対的に
高い硬さのHv:2600〜3000の最高表面硬さを
示し、一方逃げ面およびすくい面はこれより相対的に低
いHv:1800〜2200の最高表面硬さを示す表面
硬化層が形成されるようになり、このような表面硬化層
の形成されたサーメット基体の表面に、PVD法および
/またはCVD法を用いて硬質被覆層を蒸着すると、こ
の結果形成された硬質被覆層はすぐれた耐欠損性を有す
るようになり、この硬質被覆層の耐欠損性向上効果はサ
ーメット基体表面部に形成された表面硬化層の上記の硬
さ分布、すなわち切刃稜線部がHv:2600〜300
0の最高表面硬さを示し、一方逃げ面およびすくい面は
これより相対的に低いHv:1800〜2200の最高
表面硬さを示す硬さ分布によって硬質被覆層の残留圧縮
応力が著しく低減されるようになることに原因するもの
と考えられ、したがってこの結果の被覆切削チップは、
耐欠損性が要求される、例えば鋼などの高速断続切削に
用いた場合にも切刃に欠けやチッピング(微小欠け)な
どの発生なく、すくれた切削性能を長期に亘って発揮す
るという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, paying attention to the conventional coated cutting tip in which a surface hardened layer is formed on the surface of the cermet substrate,
As a result of a study aimed at improving the fracture resistance of the hard coating layer constituting the same, the content of Co and / or Ni as binder phase forming components was specified to be 7 to 17% by weight when the cermet substrate was sintered. Then, when sintering is performed under the conditions of (a) to (e), which are the above sintering conditions, the cooling atmosphere of the condition (e) is a nitrogen atmosphere of 1 to 5 torr. In the surface portion of the cermet substrate, the cutting edge ridge portion has a maximum surface hardness of Hv: 2600 to 3000, which is relatively higher than the surface hardened layer of the conventional cermet substrate, while the flank and rake face On the surface, a surface-hardened layer having a maximum surface hardness of relatively lower Hv: 1800 to 2200 is formed, and the surface of the cermet substrate on which such a surface-hardened layer is formed is subjected to PVD method and / Or CVD method When the hard coating layer is deposited by using the hard coating layer, the resulting hard coating layer has excellent fracture resistance, and the effect of improving the fracture resistance of the hard coating layer depends on the surface hardening formed on the cermet substrate surface. The above hardness distribution of the layer, that is, the cutting edge ridge portion is Hv: 2600 to 300
0, while the flank and rake face have relatively lower Hv: a hardness distribution exhibiting a maximum surface hardness of 1800 to 2200 significantly reduces the residual compressive stress of the hard coating layer. And therefore the resulting coated cutting insert is:
A study that, when used in high-speed intermittent cutting of steel, for example, requires high fracture resistance, and exhibits long-term cutting performance without chipping or chipping (small chipping) of the cutting edge. The result was obtained.
【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、結合相形成成分としてCoおよび
/またはNiを7〜17重量%含有し、Hv:1400
〜1800を示す内部硬さに対して、切刃稜線部がH
v:2600〜3000の最高表面硬さを示し、かつ逃
げ面およびすくい面がHv:1800〜2200の最高
表面硬さを示す表面硬化層が表面部に存在するサーメッ
ト基体の表面に、1〜20μmの平均層厚を有する硬質
被覆層をPVD法および/またはCVD法にて蒸着して
なる、硬質被覆層がすぐれた耐欠損性を有する被覆切削
チップに特徴を有するものである。The present invention has been made based on the above research results, and contains 7 to 17% by weight of Co and / or Ni as a binder phase forming component, and has an Hv of 1,400.
For an internal hardness of ~ 1800, the cutting edge ridge is H
v: 1-20 μm on the surface of the cermet substrate having a surface hardened layer having a maximum surface hardness of 2600-3000 and a flank face and a rake face having a maximum surface hardness of 1800-2200 Hv. The hard coating layer is characterized by being a coated cutting tip having excellent chipping resistance, obtained by depositing a hard coating layer having an average layer thickness of PVD and / or CVD.
【0006】なお、この発明の被覆切削チップを構成す
るサーメット基体の表面部に形成された表面硬化層にお
ける硬さ分布は、結合相形成成分であるCoおよび/ま
たはNiの含有量を7〜17重量%に特定した上で、上
記の通り従来被覆切削チップを構成するサーメット基体
の焼結条件である(a)〜(e)の条件のうちの(e)
条件の冷却雰囲気を1〜5torrの窒素雰囲気とした
条件で焼結を行なうことにより調整される、すなわち、
Coおよび/またはNiの含有量を前記範囲内で低く
し、かつ前記(e)条件における窒素雰囲気の圧力を前
記範囲内で高くするほど切刃稜線部と逃げ面およびすく
い面の硬さは高くなり、反対にCoおよび/またはNi
の含有量を前記範囲内で高くし、かつ窒素雰囲気の圧力
を低くするほど前記硬さは低くなるものであり、したが
って前記結合相形成成分の含有量が17重量%を越え、
かつ前記窒素雰囲気が1torr未満になると、切刃稜
線部の最高表面硬さがHv:2600未満、逃げ面およ
びすくい面の最高表面硬さがHv:1800未満となっ
てしまい、このような硬さ分布では、これに蒸着される
硬質被覆層に所望のすぐれた耐欠損性を確保することが
できなくなり、一方前記結合相形成成分の含有量が7重
量%未満にして前記窒素雰囲気が5torrを越える
と、切刃稜線部の最高表面硬さがHv:3000を越
え、かつ逃げ面およびすくい面の最高表面硬さがHv:
2200を越えるようになり、このような硬さ分布にな
っても硬質被覆層に所望の耐欠損性向上効果は見られな
いという理由によりサーメット基体における表面硬化層
の硬さ分布を上記の通りに定めたのである。また、同じ
く硬質被覆層の平均層厚を1〜20μmとしたのは、そ
の厚さが1μm未満では硬質被覆層によってもたらされ
る所望のすぐれた耐摩耗性を確保することができず、一
方その厚さが20μmを越えると耐欠損性に低下傾向が
現れるようになるという理由にもとづくものである。The hardness distribution of the hardened surface layer formed on the surface of the cermet substrate constituting the coated cutting tip according to the present invention is determined by the fact that the content of Co and / or Ni as the binder phase forming component is 7 to 17. (E) of the conditions (a) to (e), which are the sintering conditions of the cermet substrate constituting the conventional coated cutting tip as described above, after specifying the weight%.
It is adjusted by sintering under the condition that the cooling atmosphere of the condition is a nitrogen atmosphere of 1 to 5 torr, that is,
The lower the content of Co and / or Ni in the above range and the higher the pressure of the nitrogen atmosphere in the above condition (e) in the above range, the higher the hardness of the cutting edge ridge portion, the flank face and the rake face becomes. And conversely Co and / or Ni
Is higher within the above range, and the lower the pressure of the nitrogen atmosphere, the lower the hardness. Therefore, the content of the binder phase forming component exceeds 17% by weight,
And when the nitrogen atmosphere is less than 1 torr, the maximum surface hardness of the cutting edge ridge is less than Hv: 2600, and the maximum surface hardness of the flank and rake face is less than Hv: 1800. In the distribution, the hard coating layer deposited thereon cannot have the desired excellent fracture resistance, while the content of the binder phase forming component is less than 7% by weight and the nitrogen atmosphere exceeds 5 torr. And the maximum surface hardness of the cutting edge ridge line portion exceeds Hv: 3000, and the maximum surface hardness of the flank and rake face is Hv:
The hardness distribution of the surface-hardened layer in the cermet substrate is determined as described above because the hard coating layer does not have the desired effect of improving the fracture resistance even when the hardness distribution reaches such a value. It was decided. Also, the reason why the average thickness of the hard coating layer is set to 1 to 20 μm is that if the thickness is less than 1 μm, the desired excellent wear resistance provided by the hard coating layer cannot be secured. This is based on the reason that when the average particle diameter exceeds 20 μm, a tendency to decrease in fracture resistance appears.
【0007】[0007]
【発明の実施の形態】つぎに、この発明の被覆切削チッ
プを実施例により具体的に説明する。原料粉末として、
いずれも0.5〜2μmの範囲内の所定の平均粒径を有
するTiCN[重量比で(以下同じ)、TiC/TiN
=50/50]粉末、TiN粉末、TaC粉末、NbC
粉末、WC粉末、Mo2 C粉末、VC粉末、ZrC粉
末、Cr3 C2 粉末、(Ti,W,Mo)CN[Ti/
W/Mo=80/10/10、C/N=70/30]粉
末、(Ti,Ta,V)CN[Ti/Ta/V=70/
20/10、C/N=50/50]粉末、(Ti,T
a,Nb)CN[Ti/Ta/Nb=70/15/1
5、C/N=60/40]粉末、(Ti,W,Nb)C
N[Ti/W/Nb=80/10/10、C/N=70
/30]粉末、(Ti,Nb,Mo)CN[Ti/Nb
/Mo=60/30/10、C/N=60/40]粉
末、(Ti,W)CN[Ti/W=80/20、C/N
=70/30]粉末、Co粉末、およびNi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24時間湿式混合し、乾燥した後、1
ton/cm2 の圧力で圧粉体1〜13をプレス成形
し、ついでこれら圧粉体1〜13を、以下に示す条件、
すなわち室温から1300℃までを0.05torrの
真空雰囲気中、1.5℃/minの昇温速度で昇温し、
1300℃に昇温後、雰囲気を20torrの窒素雰囲
気に変えて同じ昇温速度で1500℃まで昇温し、同じ
雰囲気で1500℃に60分間保持し、最終的にそれぞ
れ1〜5torrの範囲内の所定の窒素雰囲気中で炉
冷、の条件で焼結し、焼結体に0.05mmの丸ホーニ
ングを施すことによりISO規格SNMG120408
のスローアウエイチップ形状をもったサーメット基体A
〜Mをそれぞれ製造した。また、比較の目的で、表1に
示されると同じ配合組成の圧粉体1〜13を用い、これ
の焼結を、上記の焼結条件のうちの最終工程である炉冷
をいずれも0.05torrの真空雰囲気中で行なう以
外は同じ条件でサーメット基体a〜mをそれぞれ製造し
た。DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the coated cutting insert of the present invention will be specifically described with reference to examples. As raw material powder,
In any case, TiCN having a predetermined average particle size in the range of 0.5 to 2 μm [by weight (the same applies hereinafter), TiC / TiN
= 50/50] powder, TiN powder, TaC powder, NbC
Powder, WC powder, Mo 2 C powder, VC powder, ZrC powder, Cr 3 C 2 powder, (Ti, W, Mo) CN [Ti /
W / Mo = 80/10/10, C / N = 70/30] powder, (Ti, Ta, V) CN [Ti / Ta / V = 70 /
20/10, C / N = 50/50] powder, (Ti, T
a, Nb) CN [Ti / Ta / Nb = 70/15/1
5, C / N = 60/40] powder, (Ti, W, Nb) C
N [Ti / W / Nb = 80/10/10, C / N = 70
/ 30] powder, (Ti, Nb, Mo) CN [Ti / Nb
/ Mo = 60/30/10, C / N = 60/40] powder, (Ti, W) CN [Ti / W = 80/20, C / N
= 70/30] powder, Co powder, and Ni powder were prepared, and these raw material powders were blended in the composition shown in Table 1, wet-mixed in a ball mill for 24 hours, dried, and dried.
The green compacts 1 to 13 are press-molded at a pressure of ton / cm 2 , and then these green compacts 1 to 13 are formed under the following conditions:
That is, the temperature was raised from room temperature to 1300 ° C. in a vacuum atmosphere of 0.05 torr at a rate of 1.5 ° C./min,
After the temperature was raised to 1300 ° C., the atmosphere was changed to a nitrogen atmosphere of 20 torr, the temperature was raised to 1500 ° C. at the same temperature increasing rate, and the temperature was kept at 1500 ° C. for 60 minutes in the same atmosphere. Sintering is performed in a predetermined nitrogen atmosphere under furnace cooling conditions, and a 0.05 mm round honing is performed on the sintered body to obtain an ISO standard SNMG120408.
Cermet base A with a throw-away tip shape
~ M were manufactured respectively. For the purpose of comparison, compacts 1 to 13 having the same compounding composition as shown in Table 1 were used, and the sintering of the compacts was performed in the final step of the above-mentioned sintering conditions. Cermet substrates a to m were produced under the same conditions except that the cermet substrates were performed in a vacuum atmosphere of 0.055 torr.
【0008】この結果得られた各種のサーメット基体に
ついて、表面を研磨した状態で、逃げ面およびすくい面
のHv(荷重:300g)をそれぞれ任意箇所10箇所
について測定し、また切刃稜線部は正確な表面硬さの測
定ができないので、任意箇所10箇所の研磨断面におけ
るホーニング面から0.05mm内側の位置のHv(荷
重:300g)を測定して表面硬さとし、これから最高
表面硬さを選び出し、この結果を表2、3に内部硬さと
ともに示した。With respect to various cermet substrates obtained as a result, Hv (load: 300 g) of a flank and a rake face was measured at arbitrary 10 points, respectively, while the surface was polished, and the ridge of the cutting edge was accurately measured. Since the surface hardness cannot be measured, Hv (load: 300 g) at a position 0.05 mm inside from the honing surface in the polished cross section at 10 arbitrary points is measured and determined as the surface hardness, and the maximum surface hardness is selected from this. The results are shown in Tables 2 and 3 together with the internal hardness.
【0009】ついで、上記の各種のサーメット基体の表
面に、表2、3に示される通り、(a)サーメット基体
を、アセトン中で超音波洗浄し、乾燥した状態で、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)としてそれぞれ純Ti、Ti−50重量%
Al合金、Ti−45重量%Al−5重量%Mg合金、
およびTi−40%Al−10%Cr合金を装着し、装
置内を排気して1×10-5torr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、アルゴ
ンガスを導入して1×10-3torrのアルゴンガス雰
囲気とし、この状態でサーメット基体に−800vのバ
イアス電圧を印加してサーメット基体表面をボンバート
洗浄し、ついで装置内に、硬質被覆層の組成に応じて、
反応ガスとして窒素ガス、メタンガス、または窒素ガス
とメタンガスを導入して5×10-3torrの反応雰囲
気とすると共に、前記サーメット基体に印加するバイア
ス電圧をー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、もって前記サ
ーメット基体のそれぞれの表面に、表5、6に示される
組成および平均層厚をもった硬質被覆層を形成するPV
D法、(b)通常のCVD装置を用い、表4に示される
条件にて表5、6に示される組成および平均層厚をもっ
た硬質被覆層を形成するCVD法、以上(a)または
(b)法にて硬質被覆層を形成することにより本発明被
覆切削チップ1〜13および従来被覆切削チップ1〜1
3をそれぞれ製造した。Next, as shown in Tables 2 and 3, (a) the cermet substrate was ultrasonically cleaned in acetone and dried on an arc ion plating apparatus, as shown in Tables 2 and 3. And pure Ti and Ti-50% by weight respectively as a cathode electrode (evaporation source)
Al alloy, Ti-45 wt% Al-5 wt% Mg alloy,
And a Ti-40% Al-10% Cr alloy, and while the inside of the apparatus is evacuated and kept at a vacuum of 1 × 10 −5 torr, the inside of the apparatus is heated to 500 ° C. with a heater, and then argon gas is introduced. Then, an argon gas atmosphere of 1 × 10 −3 torr was applied, and in this state, a bias voltage of −800 V was applied to the cermet substrate to bombard the surface of the cermet substrate, and then, in the apparatus, depending on the composition of the hard coating layer, ,
Nitrogen gas, methane gas, or a mixture of nitrogen gas and methane gas was introduced as a reaction gas to form a reaction atmosphere of 5 × 10 −3 torr, and the bias voltage applied to the cermet substrate was reduced to −200 V. An arc discharge is generated between the electrode and the electrode to form a hard coating layer having a composition and an average layer thickness shown in Tables 5 and 6 on each surface of the cermet substrate.
Method D, (b) CVD method of forming a hard coating layer having a composition and an average layer thickness shown in Tables 5 and 6 under the conditions shown in Table 4 using a normal CVD apparatus. By forming the hard coating layer by the method (b), the coated cutting tips 1 to 13 of the present invention and the conventional coated cutting tips 1 to 1 are formed.
3 were each manufactured.
【0010】この結果得られた各種の被覆切削チップに
ついて、 被削材:JIS・SCM440Cの長さ方向等間隔4本
縦溝入り丸棒、 切削速度:350m/min、 送り:0.2mm/rev、 切込実:1mm、 切削時間:5分、 の条件で合金鋼の高速断続切削試験を行ない、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、6に
示した。[0010] With respect to the various coated cutting tips obtained as a result, a work material: JIS SCM440C, a round bar with four longitudinal grooves at regular intervals in the longitudinal direction, a cutting speed: 350 m / min, a feed: 0.2 mm / rev A high-speed intermittent cutting test of the alloy steel was performed under the following conditions: cutting depth: 1 mm, cutting time: 5 minutes, and the flank wear width of the cutting edge was measured. Tables 5 and 6 show the results of these measurements.
【0011】[0011]
【表1】 [Table 1]
【0012】[0012]
【表2】 [Table 2]
【0013】[0013]
【表3】 [Table 3]
【0014】[0014]
【表4】 [Table 4]
【0015】[0015]
【表5】 [Table 5]
【0016】[0016]
【表6】 [Table 6]
【0017】[0017]
【発明の効果】表5、6に示される結果から、本発明被
覆切削チップ1〜13は、いずれもこれを構成するサー
メット基体の表面硬化層における相対的に高い硬さの切
刃稜線部と、相対的に硬さの低い逃げ面およびすくい面
によって、硬質被覆層はすぐれた耐欠損性を具備するよ
うになることから、苛酷な条件での切削となる鋼の高速
断続切削でも切刃に欠けやチッピングの発生なく、すぐ
れた切削性能を示すのに対して、サーメット基体の表面
硬化層に硬さ変化のない従来被覆切削チップ1〜13に
おいては、いずれも硬質被覆層の残留圧縮応力が高く、
これが原因で切刃に欠けやチッピングが発生し易く、比
較的短時間で使用寿命に至ることが明らかである。上述
のように、この発明の被覆切削チップは、これを構成す
るサーメット基体の表面硬化層における切刃稜線部の有
するHv:2600〜3000の最高表面硬さと、逃げ
面およびすくい面の有するHv:1800〜2200の
最高表面硬さの硬さ分布によって、これに形成される硬
質被覆層はすぐれた耐欠損性を有するようになるので、
例えば鋼の高速連続切削は勿論のこと、高速断続切削に
おいても切刃に欠けやチッピングの発生なく、長期に亘
ってすぐれた切削性能を発揮するのである。From the results shown in Tables 5 and 6, all of the coated cutting tips 1 to 13 of the present invention have a relatively high hardness cutting edge ridge in the surface hardened layer of the cermet substrate constituting the same. The flank and rake surfaces, which have relatively low hardness, allow the hard coating layer to have excellent fracture resistance, so it can be used as a cutting edge even in high-speed interrupted cutting of steel, which is a severe cutting condition. In the conventional coated cutting tips 1 to 13 in which the surface hardened layer of the cermet substrate has no change in hardness, while showing excellent cutting performance without occurrence of chipping or chipping, the residual compressive stress of the hard coating layer is reduced. high,
It is clear that chipping and chipping are likely to occur on the cutting blade due to this, and the service life is reached in a relatively short time. As described above, the coated cutting tip of the present invention has a maximum surface hardness of Hv: 2600-3000 and a Hv of flank and rake face of the cutting edge ridge in the surface-hardened layer of the cermet substrate constituting the coated cutting tip. Due to the hardness distribution of the highest surface hardness of 1800 to 2200, the hard coating layer formed thereon has excellent fracture resistance,
For example, not only in high-speed continuous cutting of steel but also in high-speed intermittent cutting, the cutting edge exhibits excellent cutting performance over a long period without chipping or chipping.
フロントページの続き (72)発明者 野中 勝尚 茨城県結城郡石下町大字古間木1511番地 三菱マテリアル株式会社筑波製作所内Continued on the front page (72) Inventor Katsuhisa Nonaka 1511 Furamagi, Ishishita-cho, Yuki-gun, Ibaraki Pref. Mitsubishi Materials Corporation Tsukuba Works
Claims (1)
はNiを7〜17重量%含有し、以下いずれもビッカー
ス硬さで、1400〜1800を示す内部硬さに対し
て、切刃の逃げ面とすくい面が交わる切刃稜線部が26
00〜3000の最高表面硬さを示し、かつ逃げ面およ
びすくい面が1800〜2200の最高表面硬さを示す
表面硬化層が表面部に存在する炭窒化チタン系サーメッ
トで構成された基体の表面に、1〜20μmの平均層厚
を有する硬質被覆層を物理蒸着および/または化学蒸着
してなる、硬質被覆層がすぐれた耐欠損性を有する表面
被覆サーメット製スローアウエイ型切削チップ。1. A binder having a flank of a cutting edge, which contains 7 to 17% by weight of Co and / or Ni as a binder phase forming component, and has a Vickers hardness of 1400 to 1800, respectively. 26 cutting edges where the rake faces meet
A surface hardened layer having a maximum surface hardness of 00 to 3000 and a flank and a rake surface having a maximum surface hardness of 1800 to 2200 is provided on the surface of a substrate composed of a titanium carbonitride cermet having a surface portion. A hard coating layer having an average layer thickness of 1 to 20 μm by physical vapor deposition and / or chemical vapor deposition, wherein the hard coating layer is a surface-coated cermet throw-away type cutting tip having excellent fracture resistance.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP05017097A JP3463502B2 (en) | 1997-03-05 | 1997-03-05 | Surface-coated cermet throw-away type cutting insert with a hard coating layer with excellent fracture resistance |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP05017097A JP3463502B2 (en) | 1997-03-05 | 1997-03-05 | Surface-coated cermet throw-away type cutting insert with a hard coating layer with excellent fracture resistance |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH10244406A true JPH10244406A (en) | 1998-09-14 |
JP3463502B2 JP3463502B2 (en) | 2003-11-05 |
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Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2313922A (en) * | 1995-12-22 | 1997-12-10 | Methode Electronics Inc | Massive Parallel Optical Interconnect System |
-
1997
- 1997-03-05 JP JP05017097A patent/JP3463502B2/en not_active Expired - Fee Related
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
GB2313922A (en) * | 1995-12-22 | 1997-12-10 | Methode Electronics Inc | Massive Parallel Optical Interconnect System |
GB2313922B (en) * | 1995-12-22 | 2000-06-21 | Methode Electronics Inc | Massive Parallel Optical Interconnect System |
Also Published As
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JP3463502B2 (en) | 2003-11-05 |
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