JPH0776403B2 - High hardness and high toughness cemented carbide - Google Patents
High hardness and high toughness cemented carbideInfo
- Publication number
- JPH0776403B2 JPH0776403B2 JP6540687A JP6540687A JPH0776403B2 JP H0776403 B2 JPH0776403 B2 JP H0776403B2 JP 6540687 A JP6540687 A JP 6540687A JP 6540687 A JP6540687 A JP 6540687A JP H0776403 B2 JPH0776403 B2 JP H0776403B2
- Authority
- JP
- Japan
- Prior art keywords
- hardness
- tac
- nbc
- toughness
- tic
- 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
Links
- 239000002245 particle Substances 0.000 claims description 10
- 239000012535 impurity Substances 0.000 claims description 4
- 239000000843 powder Substances 0.000 description 8
- 230000007423 decrease Effects 0.000 description 7
- 229910009043 WC-Co Inorganic materials 0.000 description 6
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 6
- 239000000463 material Substances 0.000 description 5
- 229910052723 transition metal Inorganic materials 0.000 description 4
- 238000005452 bending Methods 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000005245 sintering Methods 0.000 description 3
- 150000003624 transition metals Chemical class 0.000 description 3
- 239000000470 constituent Substances 0.000 description 2
- 230000006872 improvement Effects 0.000 description 2
- 238000012886 linear function Methods 0.000 description 2
- 150000001247 metal acetylides Chemical class 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000000611 regression analysis Methods 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000531 Co alloy Inorganic materials 0.000 description 1
- 206010053759 Growth retardation Diseases 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000000758 substrate Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- -1 transition metal carbides Chemical class 0.000 description 1
- 239000011882 ultra-fine particle Substances 0.000 description 1
- 239000002699 waste material Substances 0.000 description 1
Description
【発明の詳細な説明】 ［産業上の利用分野］ 本発明は、従来のWC−Co超硬合金より硬度及び靱性がは
るかに優れたWC−Co系超硬合金に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a WC-Co based cemented carbide which is far superior in hardness and toughness to conventional WC-Co cemented carbides.
［従来の技術］ 合金や金属等は硬度を高めると靱性が低下するという一
般的傾向を有している。しかしWC−Co系超硬合金の場合
はWCの粒度を小さくしておけば硬度を高めても靱性の低
下を抑制することができるという特性がある。この為WC
−Co系超硬合金はその高硬度性、高靱性を利用してIC基
板用加工具材等に用いられている。しかしこの様なWC−
Co系合金であっても合金製造に当り焼結工程におけるWC
の粒成長は避け難く、その結果粒径の粗大化によって粒
度の不均一を生じ硬度・靱性の両方を低下させるおそれ
がある。そこでWCの粒成長を抑制する目的でVC,TaC,Nb
C,TiC,Cr3C2等の遷移金属炭化物を少量添加することが
一般に行なわれてきた。[Prior Art] Alloys, metals and the like have a general tendency that as the hardness increases, the toughness decreases. However, in the case of WC-Co type cemented carbide, if the grain size of WC is made small, it is possible to suppress the deterioration of toughness even if the hardness is increased. Therefore WC
-Co-based cemented carbide is used as a processing tool material for IC substrates by utilizing its high hardness and high toughness. But this WC-
Even in the case of Co alloys, WC in the sintering process when manufacturing alloys
Grain growth is unavoidable, and as a result, coarsening of the grain size may cause non-uniformity of the grain size, resulting in a decrease in both hardness and toughness. Therefore, VC, TaC, Nb for the purpose of suppressing grain growth of WC
It has been common practice to add small amounts of transition metal carbides such as C, TiC, Cr 3 C 2 .
［発明が解決しようとする問題点］ しかしながら本発明者等が実験・検討を重ねた結果、特
にWCの平均粒径が1.0μｍ以下の微細なWC粉末とCo粉末
原料に前記目的で少量の上記遷移金属炭化物を添加した
ところ、実際にWCの粒成長抑制効果を生ずるのはVC及び
Cr3C2であって、NbC,TaC及びTiCは粒成長の抑制効果は
殆んど生ぜず、逆に合金の硬度或は靱性を低下させるこ
とがわかった。またVCは硬度を高めるが靱性を若干低下
させ、Cr3C2は特に靱性の向上を図る上で有効であるこ
とがわかった。[Problems to be Solved by the Invention] However, as a result of repeated experiments and studies by the present inventors, in particular, a small amount of the above WC powder and Co powder raw material having an average particle size of WC of 1.0 μm or less was used for the purpose. When transition metal carbide is added, it is VC and VC that actually produce the grain growth suppression effect of WC.
It was found that NbC, TaC and TiC, which are Cr 3 C 2 , have almost no effect of suppressing grain growth, but conversely reduce the hardness or toughness of the alloy. It was also found that VC increases hardness but slightly decreases toughness, and Cr 3 C 2 is particularly effective in improving toughness.
本発明はこの様な事情に鑑みてなされたものであって、
上記遷移金属炭化物の種類及び添加量を調整することに
よって硬度と靱性の優れたWC−Co系超硬合金を提供しよ
うとするものである。The present invention has been made in view of such circumstances,
The present invention intends to provide a WC-Co based cemented carbide having excellent hardness and toughness by adjusting the kind and addition amount of the above transition metal carbide.
［問題点を解決する為の手段］ 本発明は４％≦Co≦20％,0.2％＜VC≦２％,0.4％＜Cr3C
2≦２％,0.1＜VC/Cr3C2＜0.65（重量比）を夫々満足
し、残部が平均粒径１μｍ以下のWC及び不可避不純物か
らなるものである点に要旨を有するものである。[Means for Solving Problems] In the present invention, 4% ≦ Co ≦ 20%, 0.2% <VC ≦ 2%, 0.4% <Cr 3 C
2 ≦ 2%, 0.1 <VC / Cr 3 C 2 <0.65 (weight ratio) are satisfied, and the balance is composed of WC having an average particle size of 1 μm or less and unavoidable impurities.
また本発明は４％≦Co≦20％,0.2％＜VC≦２％,0.4％＜
Cr3C2≦２％,0.1＜VC/Cr3C2＜0.65（重量比）,0％＜TaC
＋NbC＋TiC≦0.2％を夫々満足し、残部が平均粒径１μ
ｍ以下のWC及び不可避不純物からなるものである点にも
要旨を有するものである。Further, the present invention is 4% ≦ Co ≦ 20%, 0.2% <VC ≦ 2%, 0.4% <
Cr 3 C 2 ≦ 2%, 0.1 <VC / Cr 3 C 2 <0.65 (weight ratio), 0% <TaC
+ NbC + TiC ≤ 0.2%, respectively, the balance is 1μ average particle size
It also has a gist that it consists of WC and unavoidable impurities of m or less.
［作用］ 前述の如く合金の硬度を向上させると靱性は逆に低下す
る傾向にあるが、本発明はVCを添加して硬度を向上させ
る一方、VCの添加による靱性の低下を、靱性向上効果を
有するCr3C2の添加によって補うと共に硬度或は靱性の
低下を招くおそれのあるTaC,NbC及びTiCの添加含有量を
抑制するものである。[Operation] When the hardness of the alloy is improved as described above, the toughness tends to decrease, but the present invention improves the hardness by adding VC, while the decrease in the toughness due to the addition of VC reduces the toughness. The content of TaC, NbC, and TiC, which may be compensated by the addition of Cr 3 C 2 having the property of causing a decrease in hardness or toughness, is suppressed.
添加成分の添加量限定理由は次の通りである。The reason for limiting the amount of the added component is as follows.
４％≦Co≦20％ 硬度が高く靱性が不十分なWCはCoの添加により靱性が改
善されるが、添加量が４％未満の場合は十分な添加効果
が得られず、一方20％を超すと逆に硬度が不十分とな
る。4% ≤ Co ≤ 20% WC with high hardness and insufficient toughness improves toughness due to addition of Co, but if the addition amount is less than 4%, sufficient addition effect cannot be obtained, while 20% On the contrary, if it exceeds the limit, the hardness becomes insufficient.
0.2＜VC≦２％ 添加量が0.2％以下では硬度が改善されず添加効果がな
い。一方２％を超えると靱性が不十分となる。0.2 <VC ≦ 2% If the added amount is 0.2% or less, the hardness is not improved and the effect is not obtained. On the other hand, if it exceeds 2%, the toughness becomes insufficient.
0.4％＜Cr3C2≦２％ 添加量が0.4％以下では靱性が改善されず添加効果が得
られない。一方２％を超えると硬度が不十分となる。0.4% <Cr 3 C 2 ≦ 2% If the addition amount is 0.4% or less, the toughness is not improved and the addition effect cannot be obtained. On the other hand, if it exceeds 2%, the hardness becomes insufficient.
0.1＜VC/Cr3C2＜0.65 すでに述べた様に、本発明はVCの添加による靱性の低下
をCr3C2の添加によって補うものであるが、Cr3C2の添加
量に対するVCの添加割合が0.1以下の場合は、Cr3C2の添
加割合が過剰となる結果硬度が不十分となりVCの添加効
果が得られない。一方Cr3C2に対するVCの添加割合が0.6
5以上の場合は、Cr3C2の添加割合が不十分となる結果靱
性の低下が十分に補われないこととなる。0.1 <As mentioned VC / Cr 3 C 2 <0.65 already present invention is one in which compensate for the decrease in toughness due to the addition of VC by the addition of Cr 3 C 2, the VC to the addition amount of Cr 3 C 2 When the addition ratio is 0.1 or less, the addition ratio of Cr 3 C 2 becomes excessive, resulting in insufficient hardness and the effect of adding VC cannot be obtained. On the other hand, the addition ratio of VC to Cr 3 C 2 is 0.6.
When it is 5 or more, the addition ratio of Cr 3 C 2 becomes insufficient, and as a result, the reduction in toughness is not sufficiently compensated.
０％≦TaC＋NbC＋TiC≦0.2％ これらの炭化物はすでに述べた様に、合金鋼の硬度或は
靱性を低下させるおそれがあるが、添加量の総和を0.2
％以下、より好ましくは0.1％以下に抑制すると必要な
硬度を保持したまま靱性を向上させることができる。し
かし添加量の総和が0.2％を超えると硬度或は靱性が不
十分となる。0% ≦ TaC + NbC + TiC ≦ 0.2% As described above, these carbides may reduce the hardness or toughness of the alloy steel, but the total addition amount is 0.2
% Or less, more preferably 0.1% or less, the toughness can be improved while maintaining the required hardness. However, if the total amount of addition exceeds 0.2%, the hardness or toughness becomes insufficient.
WCの平均粒径:1μｍ以下 WC−Co系超硬合金におけるWC粗大化抑制の為に遷移金属
炭化物を添加する場合、各炭化物の添加効果はWCの平均
粒径によって異なることが予想される。WC average particle size: 1 μm or less When adding a transition metal carbide to suppress WC coarsening in a WC-Co cemented carbide, it is expected that the addition effect of each carbide will vary depending on the WC average particle size.
本発明は平均粒径１μｍ以下、特に0.3〜0.8μｍの場合
に有効である。The present invention is effective when the average particle size is 1 μm or less, particularly 0.3 to 0.8 μm.
以下実施例について比較例と対比しつつ説明する。Examples will be described below in comparison with comparative examples.
［実施例］ 実施例１ 構成成分の粉末材の割合を下記の範囲で混合した24種類
の供試材からJIS抗折片をプレス成形し、1350℃で焼結
後（焼結後寸法:8×４×25mm）1300℃,2000気圧のAr雰
囲気下で熱間静水圧（HIP）処理した。[Examples] Example 1 JIS bending pieces were press-molded from 24 types of test materials in which the ratio of the powder material of the constituent components was mixed in the following range, and after sintering at 1350 ° C (size after sintering: 8 Hot isostatic pressure (HIP) treatment was performed in an Ar atmosphere at 1300 ° C. and 2000 atm.
構成成分の割合 TIC :0〜１％ TaC :0〜２％ NbC :0〜0.5％ VC :0〜２％ Cr3C2:0〜２％ Co :6〜14％ 残部:WC粉末84〜88％ WC粉末の平均粒径:0.8μｍ 得られた供試合金の組成を分析すると共に、硬度及び抗
折力を測定した。結果を第１図に示す。尚図において
◎，○，Δ及び×の印は供試合金成分が次のものである
ことを表わす。The proportion of components TIC: 0~1% TaC: 0~2% NbC: 0~0.5% VC: 0~2% Cr 3 C 2: 0~2% Co: 6~14% balance: WC powder 84-88 % WC powder average particle size: 0.8 μm The composition of the obtained match alloy was analyzed, and the hardness and transverse rupture strength were measured. The results are shown in Fig. 1. The symbols ◎, ○, Δ and × in the figure indicate that the match money components are as follows.
◎:0％≦TaC＋NbC＋TiC≦0.2％ 0.1＜VC/VCr3C2＜0.65 ○:0％≦TaC＋NbC＋TiC≦0.2％ 0.65≦VC/Cr3C2≦１ Δ:0％≦TaC＋NbC＋TiC≦0.2％ VC/Cr3C2＜0.1,又は VC/Cr3C2＞１ ×:TaC＋NbC＋TiC＞0.2％ 第１図の結果から、TaC,NbC及びTiCの総和が0.2％以下
で且つCr3C2に対するVCの比が0.1超〜0.65未満であるも
のは必要な硬度を保持しつつ靱性も優れていた。◎: 0% ≦ TaC + NbC + TiC ≦ 0.2% 0.1 <VC / VCr 3 C 2 <0.65 ○: 0% ≦ TaC + NbC + TiC ≦ 0.2% 0.65 ≦ VC / Cr 3 C 2 ≦ 1 Δ: 0% ≦ TaC + NbC + TiC ≦ 0.2% VC / Cr 3 C 2 <0.1, or VC / Cr 3 C 2 > 1 ×: TaC + NbC + TiC> 0.2% From the result of Fig. 1, the sum of TaC, NbC and TiC is 0.2% or less, and the ratio of VC to Cr 3 C 2 is Those having a hardness of more than 0.1 to less than 0.65 were excellent in toughness while maintaining the required hardness.
しかしながら、TaC,NbC及びTiCの総和が0.2％を超える
もの、或は0.2％以下であってもCr3C2に対するVCの比が
0.1以下か或は0.65以上のものは、硬度或は抗折力の少
なくともいずれか一方が不十分であった。However, even if the total sum of TaC, NbC and TiC exceeds 0.2%, or is less than 0.2%, the ratio of VC to Cr 3 C 2 is
At less than 0.1 or at least 0.65, at least one of hardness and transverse rupture strength was insufficient.
次に供試合金の硬度及び抗折力を各成分の１次関数とし
て重回帰分析した結果次の実験式（１），（２）を得
た。Next, as a result of multiple regression analysis using the hardness and transverse rupture strength of the match money as a linear function of each component, the following empirical formulas (1) and (2) were obtained.
硬度（HRA）＝94.6−0.22［％TiC］− 0.29［％TaC］−0.31［％NbC］＋ 0.35［％Cr3C2］＋0.80［％VC］− 0.33［％Co］ 相関係数Ｒ＝0.92 …（１） 抗折力（kg/mm2）＝240.3−0.45［％TiC］ −27.6［％TaC］−135.3［％NbC］＋ 28.1［％Cr3C2］−75.2［％VC］ ＋11.5［％Co］,R＝0.87 …（２） 上記（１）式より、硬度向上に対する寄与率については
VCが最も大きく次いでCr3C2であって、TaC,NbC及びTiC
の寄与率はいずれもマイナスであった。Hardness (H RA) = 94.6-0.22 [% TiC] - 0.29 [% TaC] -0.31 [% NbC] + 0.35 [% Cr 3 C 2] +0.80 [% VC] - 0.33 [% Co] Correlation coefficient R = 0.92 ... (1) transverse rupture strength (kg / mm 2) = 240.3-0.45 [% TiC] -27.6 [% TaC] -135.3 [% NbC] + 28.1 [% Cr 3 C 2] -75.2 [% VC ] +11.5 [% Co], R = 0.87 (2) From the above formula (1), regarding the contribution ratio to the hardness improvement,
VC is the largest, followed by Cr 3 C 2 , TaC, NbC and TiC
The contribution rate of each was negative.
又上記（２）式より、抗折力即ち靱性への寄与率はCr3C
2が最も大であり、VC,TaC,NbC及びTiCの寄与率はいずれ
もマイナスであった。そして抗折力よりも硬度の相関が
高かった。Also, from the above formula (2), the bending strength, that is, the contribution rate to toughness, is Cr 3 C
2 was the largest, and the contributions of VC, TaC, NbC and TiC were all negative. And the correlation of hardness was higher than the transverse rupture strength.
実施例２ 構成成分の粉末材の割合を下記の範囲で混合した21種類
の供試材を実施例１の場合と同じ条件で成形・焼結後HI
P処理をした。Example 2 21 kinds of test materials in which the ratio of the powder materials of the constituents were mixed within the following range were molded and sintered under the same conditions as in Example 1
P treated.
構成成分の割合 TaC :0〜２％ NbC :0〜0.5％ VC :0〜２％ Cr3C2:0〜２％ Co :6〜14％ 残部:WC粉末84〜88％ WC粉末の平均粒径:0.3μｍ 得られた供試合金の組成を分析すると共に、硬度及び抗
折力を測定した。その結果を第２図に示す。図中◎，
○，Δ及び×印の意味は実施例１の場合（但しTiC:0.00
2％程度）と同じである。The proportion of components TaC: 0~2% NbC: 0~0.5% VC: 0~2% Cr 3 C 2: 0~2% Co: 6~14% balance: Average grain WC powder 84 to 88% WC powder Diameter: 0.3 μm The composition of the obtained match money was analyzed, and the hardness and the transverse rupture strength were measured. The results are shown in FIG. ◎,
The meanings of ○, Δ, and × are in the case of Example 1 (however, TiC: 0.00
About 2%).
第２図の結果から明らかなように、TaC,NbC及びTiCの和
が0.2％以下で且つCr3C2に対するVCの比が0.1〜0.65で
あるものは所望の硬度が保持されしかも靱性が優れてい
た。As is clear from the results shown in FIG. 2, those in which the sum of TaC, NbC, and TiC is 0.2% or less and the ratio of VC to Cr 3 C 2 is 0.1 to 0.65 retains the desired hardness and has excellent toughness. Was there.
しかしながらTaC,NbC及びTiCの和が0.2％を超えるも
の、或は0.2％以下であっても、Cr3C2に対するVCの比が
0.1未満であるか若しくは１を超えるものは、硬度或は
抗折力の少なくともいずれか一方が不十分であった。However, even if the sum of TaC, NbC and TiC exceeds 0.2% or is less than 0.2%, the ratio of VC to Cr 3 C 2 is
If it is less than 0.1 or exceeds 1, at least one of hardness and transverse rupture strength is insufficient.
次に供試合金の硬度及び抗折力を各成分の１次関数とし
て重回帰分析した結果、次の実験式（３），（４）を得
た。Next, as a result of multiple regression analysis using the hardness and transverse rupture strength of the match money as a linear function of each component, the following empirical formulas (3) and (4) were obtained.
硬度（HRA）＝95.1−0.01［％TaC］− 0.04［％NbC］＋0.52［％Cr3C2］ ＋1.11［％VC］−0.31［％Co］ Ｒ＝0.88 …（３） 抗折力（kg/mm2＝261−30.1［％TaC］ −129［％NbC］＋35.8［％Cr3C2］ −88.4［％VC］＋9.5［％Co］ Ｒ＝0.85 …（４） 上記（３）式より硬度向上に対する寄与率についてはVC
が最も大きく、次いでCr3C2であって、TaC及びNbCの寄
与率はいずれもマイナスであった。Hardness (H RA) = 95.1-0.01 [% TaC] - 0.04 [% NbC] +0.52 [% Cr 3 C 2] +1.11 [% VC] -0.31 [% Co] R = 0.88 ... (3) anti Oriryoku (kg / mm 2 = 261-30.1 [ % TaC] -129 [% NbC] +35.8 [% Cr 3 C 2] -88.4 [% VC] +9.5 [% Co] R = 0.85 ... (4 ) From the above equation (3), the contribution ratio to hardness improvement is VC
Was the largest, followed by Cr 3 C 2 , and the contributions of TaC and NbC were both negative.
又上記（４）式より抗折力即ち靱性への寄与率はCr3C2
が最も大であり、VC,TaC,NbCの寄与率はいずれもマイナ
スであった。さらに、抗折力よりも硬度の相関の方が高
かった。次に実施例２で用いた平均粒径0.3μｍの超微
粒子超硬合金のうちCo含有量が12％の14種の供試合金を
用いて刃径６φmmのエンドミルを作成し、ダイス鋼SKD6
1を、切削速度:28m/minで切削する試験を行なった。刃
先にチッピングが生じるか或は切削屑が熱により変色し
た時点を切削長として、供試合金中に含まれるTaC,NbC
及びTiCの和が0.1未満,0.2及び2.2である場合についてV
C/Cr3C2と切削長の関係を測定した。その結果を第３図
に示す。Further, from the above formula (4), the bending strength, that is, the contribution rate to the toughness, is Cr 3 C 2
Was the largest, and the contribution rates of VC, TaC, and NbC were all negative. Furthermore, the correlation of hardness was higher than the transverse rupture strength. Next, an end mill with a blade diameter of 6φmm was prepared using 14 kinds of match alloys having a Co content of 12% of the ultrafine particle cemented carbide having an average particle diameter of 0.3 μm used in Example 2, and the die steel SKD6 was used.
A test of cutting 1 at a cutting speed of 28 m / min was performed. TaC, NbC contained in the match money is defined as the cutting length when chipping occurs on the cutting edge or when the cutting waste is discolored by heat.
And when the sum of TiC is less than 0.1, 0.2 and 2.2 V
The relationship between C / Cr 3 C 2 and cutting length was measured. The results are shown in FIG.
第３図の結果から明らかな様に、VC/Cr3C2の値が0.1〜
0.65の範囲においては、TaC,NbC及びTiCの和が0.2％の
場合は切削長は5m以上であって、エンドミルは良好な性
能を示し、TaC,NbC及びTiCの和が0.1％未満の場合は切
削7m以上となり更に性能が向上した。一方、TaC,NbC及
びTiCの和が2.2％の場合、切削長は4mとなり、エンドミ
ルの性能は不十分なものであった。As it is apparent from the results of FIG. 3, the value of VC / Cr 3 C 2 is 0.1
In the range of 0.65, when the sum of TaC, NbC and TiC is 0.2%, the cutting length is 5 m or more, the end mill shows good performance, and when the sum of TaC, NbC and TiC is less than 0.1%, Cutting was over 7 m and the performance was further improved. On the other hand, when the sum of TaC, NbC and TiC was 2.2%, the cutting length was 4 m and the performance of the end mill was insufficient.
［発明の効果］ 本発明は上記の様に構成されているから、高硬度を維持
しつつ靱性が優れたWC−Co系超硬合金を提供することが
できると共に、高価なTaCを積極的に添加することを要
しないので、製品コストの抑制をはかることができる。[Advantages of the Invention] Since the present invention is configured as described above, it is possible to provide a WC-Co type cemented carbide having excellent toughness while maintaining high hardness, and at the same time, to actively use expensive TaC. Since it does not need to be added, the product cost can be suppressed.
第１図及び第２図は本発明の実施例及び比較例における
硬度と抗折力の関係を示す図、第３図は本発明の実施例
及び比較例を用いて作成したエンドミルの切削長とTaC
＋NbC＋TiC及びVC/Cr3C2の関係を示す図である。1 and 2 are views showing the relationship between hardness and transverse rupture strength in the examples and comparative examples of the present invention, and FIG. 3 is the cutting length of the end mills prepared using the examples and comparative examples of the present invention. TaC
+ NbC + is a diagram showing the relationship between TiC and VC / Cr 3 C 2.
Claims (2)
じ）,0.2％＜VC≦２％,0.4％＜Cr3C2≦２％,0.1＜VC/Cr
3C2＜0.65（重量比）を夫々満足し、残部が平均粒径１
μｍ以下のWC及び不可避不純物からなるものであること
を特徴とする高硬度高靱性超硬合金。Claims: 1% 4% ≤ Co ≤ 20% (meaning weight%; the same applies below), 0.2% <VC ≤ 2%, 0.4% <Cr 3 C 2 ≤ 2%, 0.1 <VC / Cr
3 C 2 <0.65 (weight ratio) was satisfied, and the rest had an average particle size of 1
A high-hardness, high-toughness cemented carbide characterized by comprising WC and inevitable impurities of μm or less.
Cr3C2≦２％,0.1＜VC/Cr3C2＜0.65（重量比）,0％＜TaC
＋NbC＋TiC≦0.2％を夫々満足し、残部が平均粒径１μ
ｍ以下のWC及び不可避不純物からなるものであることを
特徴とする高硬度高靱性超硬合金。2. 4% ≦ Co ≦ 20%, 0.2% <VC ≦ 2%, 0.4% <
Cr 3 C 2 ≦ 2%, 0.1 <VC / Cr 3 C 2 <0.65 (weight ratio), 0% <TaC
+ NbC + TiC ≤ 0.2%, respectively, the balance is 1μ average particle size
A high hardness and high toughness cemented carbide characterized by comprising WC of m or less and inevitable impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6540687A JPH0776403B2 (en) | 1987-03-19 | 1987-03-19 | High hardness and high toughness cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6540687A JPH0776403B2 (en) | 1987-03-19 | 1987-03-19 | High hardness and high toughness cemented carbide |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63230846A JPS63230846A (en) | 1988-09-27 |
| JPH0776403B2 true JPH0776403B2 (en) | 1995-08-16 |
Family
ID=13286112
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6540687A Expired - Lifetime JPH0776403B2 (en) | 1987-03-19 | 1987-03-19 | High hardness and high toughness cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0776403B2 (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6452043A (en) * | 1987-08-21 | 1989-02-28 | Nachi Fujikoshi Corp | Sintered hard alloy containing superfine grain of tungsten carbide |
| CN103627942A (en) * | 2013-03-20 | 2014-03-12 | 厦门钨业股份有限公司 | Preparation method for high-performance WC-Co nanocrystal cemented carbide |
| CN103243253B (en) * | 2013-05-16 | 2016-01-20 | 成都斯锐特钨钢刀具有限公司 | Wimet and preparation method thereof |
| CN105671403B (en) * | 2016-04-15 | 2018-01-09 | 成都比拓超硬材料有限公司 | A kind of hard alloy top hammer and its on cubic hinge press synthesizing superhard material application |
| CN107955898B (en) * | 2016-10-14 | 2020-05-01 | 刘立凡 | Cemented carbide material and method for producing same |
| CN106702250B (en) * | 2016-12-21 | 2019-01-08 | 遵义中铂硬质合金有限责任公司 | A kind of hard high-strength hard alloy saw blade and its processing method |
| CN108085555A (en) * | 2017-12-04 | 2018-05-29 | 株洲夏普高新材料有限公司 | Hard alloy suitable for cutting high temperature alloy and preparation method thereof |
| CN111139389A (en) * | 2020-01-10 | 2020-05-12 | 株洲金剑硬质合金有限公司 | Preparation method of hard alloy cutter material for processing plates |
| CN111560532A (en) * | 2020-04-10 | 2020-08-21 | 河海大学 | Preparation method and application of a new type of shield machine scraper |
| CN120624910A (en) * | 2025-07-02 | 2025-09-12 | 岭南师范学院 | A WC cemented carbide and its preparation method |
-
1987
- 1987-03-19 JP JP6540687A patent/JPH0776403B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPS63230846A (en) | 1988-09-27 |
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