JPH0762185B2 - Manufacturing method of tungsten carbide based cemented carbide - Google Patents
Manufacturing method of tungsten carbide based cemented carbideInfo
- Publication number
- JPH0762185B2 JPH0762185B2 JP61094202A JP9420286A JPH0762185B2 JP H0762185 B2 JPH0762185 B2 JP H0762185B2 JP 61094202 A JP61094202 A JP 61094202A JP 9420286 A JP9420286 A JP 9420286A JP H0762185 B2 JPH0762185 B2 JP H0762185B2
- Authority
- JP
- Japan
- Prior art keywords
- powder
- based cemented
- cemented carbide
- cutting
- tungsten carbide
- 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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- Powder Metallurgy (AREA)
- Solid-Phase Diffusion Into Metallic Material Surfaces (AREA)
Description
【発明の詳細な説明】 〔産業上の利用分野〕 この発明は、耐クラツク伝幡性にすぐれ、この結果すぐ
れた耐欠損性と耐熱クラツク性を示し、かつ耐摩耗性に
もすぐれた炭化タングステン（以下WCで示す）基超硬合
金の製造法に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention has excellent resistance to crack propagation and, as a result, exhibits excellent fracture resistance and heat crack resistance, and also has excellent wear resistance. The present invention relates to a method for producing a base cemented carbide (hereinafter referred to as WC).
従来、一般に、例えば切削工具の製造に、WCを主成分と
し、必要に応じて周期律表の4a,5a,および6a族金属の炭
化物、同4aおよび5a族金属の窒化物、並びにこれらの２
種以上の固溶体などのうちの１種以上を含有し、さらに
結合相形成成分として鉄族金属のうちの１種以上、ある
いは鉄族金属と、Cr族金属およびAlなどのうちの１種以
上を含有した組成を有するWC基超硬合金が用いられてい
る。Conventionally, generally, for example, in the manufacture of cutting tools, WC as a main component, carbides of 4a, 5a, and 6a group metals of the periodic table, nitrides of 4a and 5a group metals thereof, and 2
One or more of the iron group metals, or one or more of the iron group metals and the Cr group metals and Al, etc., as a binder phase forming component. A WC-based cemented carbide having the composition contained is used.
しかし、上記の従来WC基超硬合金は、すぐれた耐摩耗性
を有するものの、これを、例えば鋼の断続切削に切削チ
ツプとして用いた場合には、切刃に欠損や熱クラツクが
発生し易く、比較的短時間で使用寿命に至るものであ
る。However, although the above conventional WC-based cemented carbide has excellent wear resistance, when this is used as a cutting chip for, for example, interrupted cutting of steel, chipping or thermal cracking of the cutting edge is likely to occur. The service life is reached in a relatively short time.
そこで、本発明者等は、上述のような観点から、上記従
来WC基超硬合金のもつ問題点を解決すべく研究を行なつ
た結果、 まず、分散相形成成分としてWCのほかに、（W,M）xCか
らイータ相（M:金属成分）が分散した組織を有するWC基
超硬合金を製造し、 ついで、このWC基超硬合金を、浸炭雰囲気、窒化雰囲
気、あるいは浸炭窒化雰囲気中、液相出現温度以上の温
度に加熱すると、前記イータ相が、WCとＭ成分とに分解
し、分解したＭ成分が他の結合相形成成分と結合して金
属結合相プールを形成するようになり、 この結果の金属結合相プールが分散した組織を有するWC
基超硬合金においては、クラツクが発生しても、その伝
幡が前記金属結合相プールによつて抑制されることか
ら、すぐれた耐欠損性と耐熱クラツク性を示すようにな
り、かつ前記金属結合相プールの存在によつて耐摩耗性
が損なわれることがないという知見を得たのである。Therefore, the present inventors, from the above viewpoints, as a result of conducting research to solve the problems of the above conventional WC-based cemented carbide, first, in addition to WC as the dispersed phase forming component, ( W, M) x C is used to produce a WC-based cemented carbide having a structure in which an eta phase (M: metal component) is dispersed, and then this WC-based cemented carbide is subjected to a carburizing atmosphere, a nitriding atmosphere, or a carbonitriding atmosphere. When heated to a temperature above the liquid phase appearance temperature, the eta phase decomposes into WC and M components, and the decomposed M components combine with other binder phase forming components to form a metal binder phase pool. And the resulting WC has a structure in which the metallic binder phase pool is dispersed.
In the base cemented carbide, even if cracks occur, the propagation of the cracks is suppressed by the metal binder phase pool, so that excellent fracture resistance and heat cracking resistance are exhibited, and We have found that the existence of the binder phase pool does not impair the wear resistance.
この発明は、上記知見にもとづいてなされたものであつ
て、以下に実施例により具体的に説明する。The present invention was made based on the above findings, and will be specifically described below with reference to examples.
実施例 １ 原料粉末として、平均粒径:3μｍを有するWC粉末、同２
μｍの金属Ｗ粉末、および同1.5μｍのCo粉末を用意
し、これら原料粉末を、重量％で、WC:86％,W:4％,Co:1
0％の配合組成に配合し、ボールミル中で48時間湿式混
合し、乾燥した後、10kg/mm2の圧力で、SNP432の切削チ
ツプ形状をもつた圧粉体にプレス成形し、ついでこの圧
粉体を、真空中、温度:1400℃に１時間保持の条件で焼
結したところ、（W,M）4Cからなる粒径が30〜70μｍの
イータ相が８容量％存在する焼結体が得られ、ついでこ
の焼結体に対して、 雰囲気ガス:CH4、 雰囲気圧力:50torr、 加熱温度:1400℃、 処理時間:1時間、 の条件で、浸炭雰囲気加熱を施すことによつて本発明法
を実施し、これによつてイータ相が全く存在せず、これ
に代つて粒径が30〜70μｍのCoに富んだ金属結合相プー
ルが９容量％の割合で分散した組織を有する本発明WC基
超硬合金製切削チツプ（以下本発明切削チツプという）
が得られた。Example 1 As a raw material powder, WC powder having an average particle diameter of 3 μm, 2
A metal W powder of μm and a Co powder of 1.5 μm are prepared, and these raw material powders are represented by weight% WC: 86%, W: 4%, Co: 1
After blending to a composition of 0%, wet-mixing in a ball mill for 48 hours, drying, press-molding with a pressure of 10 kg / mm 2 into a compact with a cutting chip shape of SNP432, and then this compact When the body was sintered in a vacuum at a temperature of 1400 ° C. for 1 hour, a sintered body containing (W, M) 4 C and having an eta phase of 8% by volume with a particle size of 30 to 70 μm was obtained. The obtained sintered body was then heated in a carburizing atmosphere under the following conditions: atmosphere gas: CH 4 , atmosphere pressure: 50 torr, heating temperature: 1400 ° C., treatment time: 1 hour. The invention is carried out by means of which the eta phase is completely absent and instead a Co-rich metal-bonded phase pool with a particle size of 30-70 μm is dispersed in a proportion of 9% by volume. WC-based cemented carbide cutting chip (hereinafter referred to as the present invention cutting chip)
was gotten.
一方、比較の目的で、配合組成を、WC:90重量％、Co:10
重量％とし、かつ浸炭処理を行なわない以外は、同一の
条件で従来WC基超硬合金製切削チツプ（以下従来切削チ
ツプという）を製造した。On the other hand, for the purpose of comparison, the composition is WC: 90% by weight, Co: 10
A conventional WC-based cemented carbide cutting chip (hereinafter referred to as a conventional cutting chip) was manufactured under the same conditions, except that the carburizing treatment was not performed in the weight percentage.
ついで、この結果の本発明切削チツプおよび従来切削チ
ツプについて、 被削材:SNCM439（硬さ:HB250）、 切削速度:100m/min、 送り:0.25mm/刃、 切込み:2mm、 の条件で鋼のフライス切削試験を行ない、切刃の欠損が
原因で使用寿命に至るまでの切削時間を測定したとこ
ろ、従来切削チツプは３分で使用寿命に達したのに対し
て、本発明切削チツプは、10分経過後も切刃に欠損の発
生は見られず、すぐれた耐欠製性を示し、さらに10分の
切削で、逃げ面摩耗幅:0.2mm、すくい面摩耗深さ:70μ
ｍのすぐれた耐摩耗性を示した。Next, regarding the cutting chip of the present invention and the conventional cutting chip of this result, under the conditions of work material: SNCM439 (hardness: H B 250), cutting speed: 100 m / min, feed: 0.25 mm / blade, depth of cut: 2 mm When the milling cutting test of steel was performed and the cutting time to the end of the service life due to the damage of the cutting edge was measured, the conventional cutting chip reached the service life in 3 minutes, whereas the cutting chip of the present invention After 10 minutes, no damage was found on the cutting edge, showing excellent chipping resistance, and after 10 minutes of cutting, flank wear width: 0.2 mm, rake wear depth: 70 μ
m showed excellent wear resistance.
実施例 ２ 原料粉末として、平均粒径:5μｍのWC粉末、同3.5μｍ
のW2C粉末、同２μｍのTiC粉末、同２μｍのTiN粉末、
同1.5μｍのNbC粉末、同1.5μｍのTaC粉末、および同1.
5μｍのCo粉末を用い、これら原料粉末を、重量％でWC:
83％,W2C:5％、TiC:2％、TiN:1％、TaC:3％、NbC:1％、
Co:5％の配合組成に配合する以外は、実施例１における
と同一の条件で混合し、乾燥し、プレス成形し、ついで
焼結して、（W,N）6Cからなる粒径が10〜20μｍのイー
タ相が10容量％の割合で分散した組織を有するWC超硬硬
金を製造し、ついで、これに対して、 雰囲気ガス:N2、 雰囲気圧力:100torr、 温度:1400℃、 処理時間:1時間、 の条件で窒化雰囲気加熱を施すことによつて本発明法を
実施し、これによつて、イータ相が存在せず、これに代
つて粒径が10〜20μｍのCoに富んだ金属結合相プールが
10容量％の割合で分散した組織を有する本発明切削チツ
プが製造された。Example 2 As a raw material powder, WC powder having an average particle size of 5 μm, the same as 3.5 μm
W 2 C powder, the same 2 μm TiC powder, the same 2 μm TiN powder,
Same 1.5 μm NbC powder, same 1.5 μm TaC powder, and 1.
Using Co powder of 5 μm, these raw material powders in WC by weight%:
83%, W 2 C: 5%, TiC: 2%, TiN: 1%, TaC: 3%, NbC: 1%,
Mixing was performed under the same conditions as in Example 1 except that the composition was Co: 5%, and the mixture was dried, press-molded, and then sintered to obtain a particle size of (W, N) 6 C. WC cemented carbide having a structure in which an eta phase of 10 to 20 μm is dispersed at a ratio of 10% by volume is manufactured, and then, against this, atmospheric gas: N 2 , atmospheric pressure: 100 torr, temperature: 1400 ° C., Treatment time: 1 hour, the method of the present invention was carried out by heating in a nitriding atmosphere, whereby the eta phase was absent and, instead, Co having a particle size of 10 to 20 μm was obtained. Rich metal bonded phase pool
Cutting chips according to the invention having a texture dispersed at a rate of 10% by volume were produced.
また、実施例１におけると同様に、配合組成を、重量％
で、WC:88％、TiC:2％、TiN:1％、TaC:3％、NbC:1％、C
o:5％とし、かつ窒化処理を行なわない以外は、同一の
条件で従来切削チツプを製造した。Further, as in Example 1, the blending composition was changed to wt%.
, WC: 88%, TiC: 2%, TiN: 1%, TaC: 3%, NbC: 1%, C
A conventional cutting chip was manufactured under the same conditions except that o: 5% and no nitriding treatment was performed.
この結果得られた本発明切削チツプと従来切削チツプに
ついて、実施例１におけると同一の条件で鋼のフライス
切削試験を行なつたところ、従来切削チツプは0.5分で
切刃に欠損を生じ、使用寿命に至つたのに対して、本発
明切削チツプは、10分経過後も切刃に欠損発生は見られ
ず、引続いての使用が可能な、すぐれた耐摩耗性と、す
ぐれた耐欠損性および耐熱クラツク性を示すものであつ
た。With respect to the cutting chip of the present invention and the conventional cutting chip obtained as a result, a milling test of steel was conducted under the same conditions as in Example 1. The conventional cutting chip had a cutting edge defect in 0.5 minutes and was used. On the other hand, the cutting tip of the present invention has reached the end of its life, and no damage is found on the cutting edge even after 10 minutes have passed, and it can be used continuously and has excellent wear resistance and excellent damage resistance. And showed heat-resistant cracking resistance.
実施例 ３ 原料粉末として、平均粒径:3μｍを有するWC粉末、同３
μｍのTiH2粉末、同２μｍのTiC粉末、同1.5μｍのTaC
粉末、および1.5μｍのCo粉末を用意し、これら原料粉
末を、重量％で、WC:85％、TiH2:3％、TiC:5％、TaC:2
％、Co:5％の配合組成に配合する以外は、実施例１にお
けると同一の条件で混合し、乾燥し、プレス成形し、つ
いで焼結して、（W,M）6Cからなり、かつ幅:10〜30μｍ
×長さ:150〜300μｍの寸法をもつたイータ相が15容量
％の割合で分散した組織を有するWC基超硬合金を製造
し、ついで、これに対して、 雰囲気ガス:N2＋Co（1:1）、 雰囲気圧力:100torr、 温度:1400℃、 処理時間:1時間、 の条件で浸炭窒化雰囲気加熱を施すことによつて本発明
法を実施し、イータ相が存在せず、これに代つて幅:10
〜40μｍ×長さ:120〜160μｍの寸法を有するCoに富ん
だ金属結合相プールが17容量％の割合で分散した組織を
有する本発明切削チツプを製造した。Example 3 As a raw material powder, WC powder having an average particle diameter of 3 μm,
μm TiH 2 powder, 2 μm TiC powder, 1.5 μm TaC
Prepare powder and Co powder of 1.5 μm, and use these raw material powders in weight% as follows: WC: 85%, TiH 2 : 3%, TiC: 5%, TaC: 2
%, Co: 5%, but mixed in the same conditions as in Example 1, dried, press molded, then sintered to consist of (W, M) 6 C, And width: 10 to 30 μm
× Length: A WC-based cemented carbide having a structure in which an eta phase having a size of 150 to 300 μm is dispersed at a ratio of 15% by volume, and then an atmosphere gas: N 2 + Co (1 1), atmospheric pressure: 100 torr, temperature: 1400 ° C., treatment time: 1 hour, the method of the present invention was carried out by heating in a carbonitriding atmosphere, and the eta phase was not present. Width: 10
A cutting chip of the invention having a texture in which a Co-rich metal-bonded phase pool having a size of ˜40 μm × length: 120-160 μm was dispersed in a proportion of 17% by volume was produced.
また、比較の目的で配合組成を、重量％で、WC:88％、T
iC:5％、TaC:2％、Co:5％とし、かつ浸炭窒化処理を行
なわない以外は同一の条件で従来切削チツプを製造し
た。In addition, for the purpose of comparison, the composition of the composition is% by weight, WC: 88%, T
A conventional cutting chip was manufactured under the same conditions except that iC: 5%, TaC: 2%, Co: 5%, and that carbonitriding was not performed.
これらの切削チツプについて、実施例１におけると同一
の条件で鋼のフライス切削試験を行なつたところ、従来
切削チツプは３分で切刃欠損が発生し使用寿命に至つた
のに対して、本発明切削チツプは10分経過後も切刃に欠
損の発生は見られず、さらに引続いての使用が可能であ
つた。When these steel chips were subjected to a milling cutting test of steel under the same conditions as in Example 1, the conventional cutting chips had a cutting edge defect in 3 minutes and reached the end of their service life. After 10 minutes, the cutting chip did not show any damage to the cutting edge and could be used continuously.
実施例 ４ 原料粉末として、平均粒径:3μｍのWC粉末、同２μｍの
Cr3O2粉末、同２μｍのVO5粉末、同１μｍのＷ粉末、お
よび同1.5μｍのCo粉末を用い、これら原料粉末を、WC:
91.8％、W:0.2％、Cr3O2:2％、VO5:1％、Co:5％の配合
組成に配合する以外は、実施例１におけると同一の条件
で混合し、乾燥し、プレス成形し、ついで焼結して、
（W,M）6Cからなる粒径が20〜30μｍのイータ相が17容
量％の割合で分散した組織を有するWC基超硬合金を製造
し、ついて、これに対して、 雰囲気ガス:CH4、 雰囲気圧力:200torr、 温度:1400℃、 処理時間:2時間、 の条件で浸炭雰囲気加熱を施すことによつて本発明法を
実施し、イータ相が存在せず、これに代つて粒径が30〜
40μｍのCoに富んだ金属結合相プールが17容量％の割合
で分散した組織を有する本発明切削チツプを製造した。Example 4 As a raw material powder, WC powder having an average particle size of 3 μm and powder having an average particle size of 2 μm
Using Cr 3 O 2 powder, VO 5 powder of 2 μm, W powder of 1 μm, and Co powder of 1.5 μm, these raw material powders were WC:
91.8%, W: 0.2%, Cr 3 O 2: 2%, VO 5: 1%, Co: except that blending of 5% of the formulation composition was mixed under the same conditions as in Example 1, dried, Press molding, then sintering,
A WC-based cemented carbide having a structure in which an eta phase composed of (W, M) 6 C and having a particle size of 20 to 30 μm is dispersed at a ratio of 17% by volume is prepared. 4, the ambient pressure: 200 torr, temperature: 1400 ° C., treatment time: 2 hours, by connexion present invention method is subjected to a carburizing atmosphere heated at conditions of conducted, there is no eta phase, Daitsute particle size to Is 30 ~
A cutting chip of the present invention having a structure in which a 40 μm Co-rich metal bonded phase pool was dispersed at a rate of 17% by volume was produced.
この本発明切削チツプについて、実施例１におけると同
一の条件で鋼のフライス切削試験を行ない、切刃の逃げ
面磨耗幅が0.3mmに至るまでの切削時間を測定したとこ
ろ、15分を示し、この場合も切刃に欠損発生は全く見ら
れなかつた。With respect to this cutting chip of the present invention, a milling test of steel was performed under the same conditions as in Example 1, and the cutting time until the flank wear width of the cutting edge reached to 0.3 mm was measured, showing 15 minutes, In this case as well, no defect was found on the cutting edge.
上記実施例１〜４の結果から、本発明切削チツプは、金
属結合相プールの形成がない従来切削チツプに比して、
耐欠損性および耐熱クラツク性にすぐれ、かつすぐれた
耐摩耗性を示すことが明らかである。From the results of Examples 1 to 4 described above, the cutting chip of the present invention is superior to the conventional cutting chip in which the metal binder phase pool is not formed,
It is clear that it has excellent fracture resistance and heat cracking resistance, and also has excellent wear resistance.
上述のように、この発明の方法によれば、耐クラツク伝
幡抑制作用のある金属結合相プールの形成によつて、す
ぐれた耐欠損性と耐熱クラツク性を有し、かつ耐摩耗性
にもすぐれたWC基超硬合金を製造することができるので
ある。As described above, according to the method of the present invention, due to the formation of the metal binder phase pool having an effect of suppressing crack propagation, it has excellent fracture resistance and heat crack resistance, and also has wear resistance. It is possible to produce excellent WC-based cemented carbide.
Claims (1)
M）xCからなるイータ相（M:金属成分）が分散した組織
を有する炭化タングステン基超硬合金を製造し、 （ｂ） ついで、この炭化タングステン基超硬合金を、
浸炭雰囲気、窒化雰囲気、あるいは浸炭窒化雰囲気中、
液相出現温度以上の温度に加熱して、前記イータ相を、
炭化タングステンと、クラック伝幡抑制作用を有する金
属結合相プールとに分解すること、 を特徴とする耐クラック伝幡性のすぐれた炭化タングス
テン基超硬合金の製造法。1. In addition to (a) tungsten carbide, (W,
(M) x C to produce a tungsten carbide-based cemented carbide having a structure in which an eta phase (M: metal component) is dispersed, and (b)
In a carburizing atmosphere, a nitriding atmosphere, or a carbonitriding atmosphere,
By heating to a temperature above the liquid phase appearance temperature, the eta phase,
A method for producing a tungsten carbide-based cemented carbide having excellent crack propagation resistance, which comprises decomposing into tungsten carbide and a metal binder phase pool having an effect of suppressing crack propagation.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61094202A JPH0762185B2 (en) | 1986-04-23 | 1986-04-23 | Manufacturing method of tungsten carbide based cemented carbide |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61094202A JPH0762185B2 (en) | 1986-04-23 | 1986-04-23 | Manufacturing method of tungsten carbide based cemented carbide |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62250134A JPS62250134A (en) | 1987-10-31 |
| JPH0762185B2 true JPH0762185B2 (en) | 1995-07-05 |
Family
ID=14103714
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61094202A Expired - Fee Related JPH0762185B2 (en) | 1986-04-23 | 1986-04-23 | Manufacturing method of tungsten carbide based cemented carbide |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0762185B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002210525A (en) * | 2001-01-12 | 2002-07-30 | Denso Corp | Carbide tool |
| JP6515387B2 (en) * | 2015-09-15 | 2019-05-22 | 日本製鉄株式会社 | Carbide tool and method of manufacturing the same |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5284108A (en) * | 1975-12-30 | 1977-07-13 | Seiko Epson Corp | Super alloy |
| JPS55107754A (en) * | 1979-02-13 | 1980-08-19 | Mitsubishi Metal Corp | Tungsten carbide-base sintered hard alloy |
-
1986
- 1986-04-23 JP JP61094202A patent/JPH0762185B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62250134A (en) | 1987-10-31 |
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