JPS61159557A - Powdery high-speed steel - Google Patents
Powdery high-speed steelInfo
- Publication number
- JPS61159557A JPS61159557A JP27913784A JP27913784A JPS61159557A JP S61159557 A JPS61159557 A JP S61159557A JP 27913784 A JP27913784 A JP 27913784A JP 27913784 A JP27913784 A JP 27913784A JP S61159557 A JPS61159557 A JP S61159557A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- toughness
- wear resistance
- speed
- 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.)
- Pending
Links
Abstract
Description
発明の目的 Purpose of invention
本発明は、粉末高速度工具鋼の改良に関する。
[従来の技術]
高速度工具鋼において重要な特性である耐摩耗性や硬さ
を高めるためには1、一般に高合金組成をえらぶことか
有利である。 ところが、高合金組成のものを溶解−鋳
造により製造すると、炭化物の粒子が粗大になりやすく
、靭性が低下するので、粉末冶金法によることが得策で
ある。
しかし、焼結鋼においても焼入れ時の炭化物の粗大化は
多少は起るので、上記した特性の向上には自ら限界があ
り、粉末冶金法の利点を生かすためには、各合金成分の
作用と添加量との関係を十分に考慮し、バランスのよい
組成を選択する必要がある。The present invention relates to improvements in powdered high speed tool steel. [Prior Art] In order to improve wear resistance and hardness, which are important properties in high-speed tool steel, it is generally advantageous to select a high alloy composition. However, if a material with a high alloy composition is manufactured by melting and casting, the carbide particles tend to become coarse and the toughness decreases, so it is advisable to use a powder metallurgy method. However, even in sintered steel, coarsening of carbides occurs to some extent during quenching, so there is a limit to the improvement of the above-mentioned properties, and in order to take advantage of the advantages of powder metallurgy, it is necessary to It is necessary to carefully consider the relationship with the amount added and select a well-balanced composition.
本発明の目的は、上記の観点から行なった注意深い合金
設計にもとづき、いっそう改善された耐摩耗性および硬
さを有し、しかも靭性その他の特性は低下していない粉
末高速度鋼を提供することにある。
発明の構成
[問題点を解決するための手段]
本発明の改良された粉末高速度工具鋼は、8−Go工具
鋼の領域において、下記の組成すなりら、C:1.65
〜1.80%、Si :0.40%以下、Mn :Q
、40%以下、Cr :3.80〜4.50%、Mo
:4.50〜5.50%、W:7.3〜8.5%、V:
4.50〜5.50%および’Co : 7.00〜9
.00%を含有し、P:0.030%以下、S:0.0
30%以下、Cu:0.25%以下、Ni :0.2
5%以下でおって残部がFeである合金組成をえらび、
この合金の粉末を成形し焼結してなるものである。An object of the present invention is to provide a powdered high-speed steel having further improved wear resistance and hardness, with no reduction in toughness or other properties, based on careful alloy design carried out from the above viewpoints. It is in. Structure of the Invention [Means for Solving the Problems] The improved powder high speed tool steel of the present invention has the following composition in the area of 8-Go tool steel: C: 1.65
~1.80%, Si: 0.40% or less, Mn: Q
, 40% or less, Cr: 3.80-4.50%, Mo
:4.50~5.50%, W:7.3~8.5%, V:
4.50-5.50% and 'Co: 7.00-9
.. 00%, P: 0.030% or less, S: 0.0
30% or less, Cu: 0.25% or less, Ni: 0.2
Selecting an alloy composition in which the content is 5% or less and the balance is Fe,
It is made by molding and sintering the powder of this alloy.
上記の組成は、前述のように各合金成分のバランスを検
討して決定したものであるが、最大の特徴は、比較的低
目におさえたMOと高目にえらんだWのバランスにある
。耐摩耗性などの指標としてよく知られているタングス
テン当量の式、W%+2MO%
においで、MOはWの2倍の影響力をもつから、当量の
値を大きくするには、Mo含有量を高めるのが効果的と
いうことになる。 しかし、熱間加工性および焼入れ時
の炭化物の粗大化傾向は、W炭化物の方がMO炭化物よ
り小さいことがわかったので、本発明ではその事実を利
用して、W含有量を高くすることにより、靭性の低下を
避けて耐摩耗性と高温硬さとを向上させたわけである。
各合金元素の作用と、成分組成の限定理由は次のとおり
である。
Mo :4.50〜5.50%
WとともにMeC型の炭化物を形成して、切削性と耐摩
耗性に寄与する。 この効果を得るためには4.50%
以上の添加が必要でおり、一方で前述した熱間加工時お
よび焼入れ時における炭化物の粗大化による害をおさえ
るため、5.50%を超えない添加量に止める。
Wニア。3〜8.5%
1v1oと共同して、炭化物が切削性と耐摩耗性を与え
る。 炭化物が粗大化しにくい点を利用して、低目にお
さえられたMOの代りにはたらかせるため、7.5%以
上を添加する。 上限は、靭性の低下と、材料”価格の
点から定めた。
Cr :3.80〜4.50%
下限は焼入性の確保のため必要でおり、上限は靭性の低
下を配慮して定めたものであ”る。
V :・4.50〜5.50%
低摩擦領域の耐摩耗性を保つために添加する。過大にな
ると炭化物の巨大品が析出して靭性を損うので、上記の
範囲内とする。
Co:7.OO〜9.00%
WとMOのマトリクスへの固溶を助け、耐熱性を高める
。 7.00%以上添加しないと焼もどし硬さが不足し
、一方で9゜00%を超えて添加しても効果は高まらず
、靭性の低下を招く。
C:1.65〜1.80%
W、MO、CrおよびVの炭化物の形成に必須であり、
かつそれ自身マトリクスに固溶して高い焼戻し硬さを与
える。 理想的な量は、次式の「カーボン当量」として
算出できる。
C%=0.06Cr +0.033W
+0.063Mo +0.20V
上記のほかの元素は、原料中に通常含まれる脱酸剤また
は不純物であって、上限の数字はその許容量である。
、The above composition was determined by examining the balance of each alloy component as described above, but the most important feature lies in the balance between relatively low MO and high W. In the formula for tungsten equivalent, W% + 2MO%, which is well known as an index of wear resistance, MO has twice the influence of W, so to increase the equivalent value, increase the Mo content. It is effective to increase it. However, it has been found that hot workability and the coarsening tendency of carbides during quenching are smaller in W carbides than in MO carbides, so in the present invention, we take advantage of this fact by increasing the W content. This improves wear resistance and high-temperature hardness while avoiding a decrease in toughness. The effects of each alloying element and the reasons for limiting the composition are as follows. Mo: 4.50-5.50% Forms MeC type carbide together with W, contributing to machinability and wear resistance. To obtain this effect, 4.50%
On the other hand, in order to suppress the damage caused by coarsening of carbides during hot working and quenching, the addition amount is limited to no more than 5.50%. W near. In conjunction with 3-8.5% 1v1o, carbides provide machinability and wear resistance. Taking advantage of the fact that carbides are difficult to coarsen, 7.5% or more of MO is added in order to work in place of MO, which is kept at a low level. The upper limit was determined in consideration of the decrease in toughness and material price. Cr: 3.80 to 4.50% The lower limit is necessary to ensure hardenability, and the upper limit was determined in consideration of the decrease in toughness. There are many things. V: 4.50 to 5.50% Added to maintain wear resistance in low friction areas. If it becomes too large, huge carbide particles will precipitate, impairing toughness, so it should be within the above range. Co:7. OO~9.00% Helps solid solution of W and MO into the matrix and improves heat resistance. If it is not added in an amount of 7.00% or more, the tempering hardness will be insufficient, while if it is added in an amount exceeding 9.00%, the effect will not be enhanced and the toughness will decrease. C: 1.65-1.80% Essential for the formation of W, MO, Cr and V carbides,
In addition, it dissolves itself in the matrix to provide high tempering hardness. The ideal amount can be calculated as the "carbon equivalent" of the following formula. C%=0.06Cr +0.033W +0.063Mo +0.20V The other elements mentioned above are deoxidizing agents or impurities normally contained in the raw materials, and the upper limit number is the allowable amount thereof. ,
下記の成分組成の鋼を溶解し、窒素ガスジェット流で噴
霧し、ふるい分けて種々の粒度の合金粉末を用意した。
比較例は、従来品でめる。
Nα 1 2 3 比較例C1,681
,711,661,2&
S i O,310,290,310,22Na
1 2 3 比較例Mn
O,280,300,330,24P O,
0150,0120,0090,009S O,
0130,0100,0110,010CIJ
O,0B 0.0B 0.09 0.04
N i O,090,070,080,06Cr
4.33 4.17 4.06 4.
llMo 4.58 5.39 4.67
4.98W 8.41 7.88 7.
49 6.40V 4.52 5.24
4.88 3.12Co 8.01 7
.44 8.72 8.44合金粉末を配合し、
径120mmの軟m製カプセルに充填し、脱気、密封し
て熱間で鍛造した。
続いて、鍛造した材料に対し、つぎの熱処理を施した。
焼入れ:1,210’CXa分間→油冷焼戻し: 5
50℃×1時間→空冷(3回)熱処理後の材料について
ミクロ組織をしらべたところ、十分に微細であって、粗
大または巨大品の生成は認められなかった。 また、炭
化物含有量を電解抽出法により測定して、それぞれつぎ
の結果を1qた。
本発明Nα1〜3 19.5〜22.4%比較例
12.4%硬さおよび靭性の測定結
果は、つぎのとおりておる。
NQ 1 2 3 比較例硬
さ 68.2 67.8 68.0
66.7(HRc)
抗折力 417 420 422 37B<
Kyf/lNn2)
比摩耗量を、下記の条件の人感式摩耗試験によってしら
べた。
回転円板:30M21 (SA)
最終荷重:6.5に9
摩擦速度: 2.86m/sec
摩擦距離:200m
その結果はつぎのとおりであって、比摩耗量が全般に小
さく、とくに低摩擦速度領域においてこの高速度鋼がす
ぐれていることがわかる。
No、 1 2 3 止較舅比摩
耗量 0.96 0.98 1.02 1.8
2次に、比研削性を下記の条件で試験した。
砥 石:WA#120
切込み 〜0.5履
送 リ:0.02m/ストローク
砥石周速: 1370TrL/min
研削比すなわち(被研削量/砥石摩耗量)はつぎのとお
りである。
NQ 1 2 3 迄鮫画研削比 6
.91 7.51 7.98 5.42最後に
、本発明の粉末高速度鋼で切削工具をつくり、下記の条
件の断続切削試験を行なって、実用性能をしらべた。
送 リ: 0.05s/rev。
切込み :5ffill+
切削速度: 6C)〜52m/min
切削材 :80M420 (N>
歯車 m=2.5 2=31
φ=82.5
つぎのデータが得られた。
NQ 1 2 3 比較例最大フランク0
.55 0.51 0.47 0.63摩耗(s
)
発明の効果
本発明の粉末高速度工具鋼は、注意深く選択し、とくに
従来品にくらべてMO含有量を低くしW含有量を高くし
た合金組成をえらぶことにより、熱間加工時および焼入
れ時の炭化物粒子の粗大化をおさえることに成功したも
のでおる。 これによって、焼結鋼の利点が十分に生か
され、靭性の低下を伴うことなくいっそう高められた耐
摩耗性と高温硬さとをもった工具鋼が提供される。Steel having the following composition was melted, sprayed with a nitrogen gas jet stream, and sieved to prepare alloy powders of various particle sizes. The comparative example is a conventional product. Nα 1 2 3 Comparative example C1,681
,711,661,2&S i O,310,290,310,22Na
1 2 3 Comparative example Mn
O, 280, 300, 330, 24P O,
0150,0120,0090,009SO,
0130,0100,0110,010CIJ
O,0B 0.0B 0.09 0.04
N i O,090,070,080,06Cr
4.33 4.17 4.06 4.
llMo 4.58 5.39 4.67
4.98W 8.41 7.88 7.
49 6.40V 4.52 5.24
4.88 3.12Co 8.01 7
.. 44 8.72 8.44 Blending alloy powder,
It was filled into a soft m capsule with a diameter of 120 mm, degassed, sealed, and hot forged. Subsequently, the forged material was subjected to the following heat treatment. Quenching: 1,210'CXa minutes → Oil-cooled tempering: 5
When the microstructure of the material after heat treatment at 50° C. for 1 hour → air cooling (3 times) was examined, it was found to be sufficiently fine and no formation of coarse or giant products was observed. In addition, the carbide content was measured by electrolytic extraction, and the following results were obtained for 1 q. Invention Nα1-3 19.5-22.4% Comparative example
The measurement results of 12.4% hardness and toughness are as follows. NQ 1 2 3 Comparative example hard
Sa 68.2 67.8 68.0
66.7 (HRc) Transverse rupture strength 417 420 422 37B<
Kyf/lNn2) The specific wear amount was determined by a human wear test under the following conditions. Rotating disk: 30M21 (SA) Final load: 6.5 to 9 Friction speed: 2.86m/sec Friction distance: 200m The results are as follows, and the specific wear amount is generally small, especially in the low friction speed region It can be seen that this high-speed steel is excellent. No. 1 2 3 Amount of wear compared to the toe at rest 0.96 0.98 1.02 1.8
Second, specific grindability was tested under the following conditions. Grinding wheel: WA#120 Depth of cut ~0.5 feed Re: 0.02 m/stroke Grinding wheel circumferential speed: 1370 TrL/min The grinding ratio, that is, (amount to be ground/amount of grinding wheel wear) is as follows. Shark drawing ratio up to NQ 1 2 3 6
.. 91 7.51 7.98 5.42 Finally, a cutting tool was made from the powdered high-speed steel of the present invention, and an interrupted cutting test was conducted under the following conditions to examine its practical performance. Feedback: 0.05s/rev. Depth of cut: 5ffill+ Cutting speed: 6C)~52m/min Cutting material: 80M420 (N> Gear m=2.5 2=31 φ=82.5 The following data were obtained. NQ 1 2 3 Comparative example maximum flank 0
.. 55 0.51 0.47 0.63 Wear (s
) Effects of the Invention By carefully selecting the powder high-speed tool steel of the present invention, and in particular selecting an alloy composition with a lower MO content and higher W content than conventional products, the powder high-speed tool steel has improved performance during hot working and quenching. We succeeded in suppressing the coarsening of carbide particles. This makes full use of the advantages of sintered steel, providing a tool steel with even higher wear resistance and high-temperature hardness without deterioration in toughness.
Claims (1)
n:0.40%以下、Cr:3.80〜4.50%、M
o:4.50〜5.50%、W:7.3〜8.5%、V
:4.50〜5.50%およびCo:7.00〜9.0
0%を含有し、P:0.030%以下、S:0.030
%以下、Cu:0.25%以下、Ni:0.25%以下
であつて、残部がFeである合金の粉末を成形し焼結し
てなる高速度工具鋼。C: 1.65-1.80%, Si: 0.40% or less, M
n: 0.40% or less, Cr: 3.80-4.50%, M
o: 4.50-5.50%, W: 7.3-8.5%, V
:4.50~5.50% and Co:7.00~9.0
Contains 0%, P: 0.030% or less, S: 0.030
% or less, Cu: 0.25% or less, Ni: 0.25% or less, and the balance is Fe.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27913784A JPS61159557A (en) | 1984-12-29 | 1984-12-29 | Powdery high-speed steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP27913784A JPS61159557A (en) | 1984-12-29 | 1984-12-29 | Powdery high-speed steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPS61159557A true JPS61159557A (en) | 1986-07-19 |
Family
ID=17606944
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP27913784A Pending JPS61159557A (en) | 1984-12-29 | 1984-12-29 | Powdery high-speed steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS61159557A (en) |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111118383A (en) * | 2019-12-12 | 2020-05-08 | 北京机科国创轻量化科学研究院有限公司 | Powder steel and preparation method thereof |
CN111136276A (en) * | 2019-12-12 | 2020-05-12 | 北京机科国创轻量化科学研究院有限公司 | Preparation method of high-speed steel cutter |
-
1984
- 1984-12-29 JP JP27913784A patent/JPS61159557A/en active Pending
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN111118383A (en) * | 2019-12-12 | 2020-05-08 | 北京机科国创轻量化科学研究院有限公司 | Powder steel and preparation method thereof |
CN111136276A (en) * | 2019-12-12 | 2020-05-12 | 北京机科国创轻量化科学研究院有限公司 | Preparation method of high-speed steel cutter |
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