JPH02182867A - Powdered tool steel - Google Patents
Powdered tool steelInfo
- Publication number
- JPH02182867A JPH02182867A JP99389A JP99389A JPH02182867A JP H02182867 A JPH02182867 A JP H02182867A JP 99389 A JP99389 A JP 99389A JP 99389 A JP99389 A JP 99389A JP H02182867 A JPH02182867 A JP H02182867A
- Authority
- JP
- Japan
- Prior art keywords
- tool steel
- weq
- hardenability
- toughness
- condition
- 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
- 229910001315 Tool steel Inorganic materials 0.000 title claims abstract description 21
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 8
- 239000000956 alloy Substances 0.000 claims abstract description 8
- 229910052721 tungsten Inorganic materials 0.000 claims abstract description 7
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 4
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 4
- 239000000843 powder Substances 0.000 claims description 15
- 229910052742 iron Inorganic materials 0.000 claims description 2
- 238000005482 strain hardening Methods 0.000 abstract description 6
- 229910000831 Steel Inorganic materials 0.000 abstract description 5
- 239000010959 steel Substances 0.000 abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 4
- 229910052748 manganese Inorganic materials 0.000 abstract description 3
- 150000001247 metal acetylides Chemical class 0.000 description 9
- 239000000463 material Substances 0.000 description 8
- 230000000694 effects Effects 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 238000001816 cooling Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 229910001563 bainite Inorganic materials 0.000 description 3
- 238000005516 engineering process Methods 0.000 description 3
- 230000000171 quenching effect Effects 0.000 description 3
- 238000005299 abrasion Methods 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 238000005496 tempering Methods 0.000 description 2
- 229910003178 Mo2C Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000010273 cold forging Methods 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 229910052738 indium Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 238000004663 powder metallurgy Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000000523 sample Substances 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000005507 spraying Methods 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
本発明は、苛酷な条件下に使用される冷間加工工具をつ
くるための粉末工具鋼の改良に関する。
この粉末工具鋼は、焼入性にすぐれ高硬度で、しかも高
靭性を有する。The present invention relates to improvements in powder tool steel for making cold work tools used under severe conditions. This powder tool steel has excellent hardenability, high hardness, and high toughness.
冷間加工工具の材料として、溶製材では従来、ＪＩＳの
５ＫＨ５１を代表とする冷間工具鋼が使用されてきた。
この鋼は、耐摩耗性にすぐれ、靭性も比較的高く、冷
間の精密加工用金型に適する材料である。
ところが、近年の冷間加工工具の大型化や精密化の傾向
、たとえば大型の冷間鍛造型に対する需要の増大や、後
型のクリヤランスを小さくしたいという希望が強くなる
に伴い、熱処理に歪みの少い真空熱処理が多用されるよ
うになった。 真空熱処理は、冷却をガスによって行な
うので冷却速度を高くすることができず、処理対象の大
型化による質量効果の問題もあって、焼入効果が不足し
がちである。 このため、焼入性が高く、耐摩耗で高靭
性の材料が要求されるようになってきた。
この要求に対して、５ＫＨ５１では硬さと耐摩耗性が不
足でこたえきれないし、焼入性も低い。
５ＫＨ５１は、焼入性を左右するＣｒ含有量が４％程度
（３，８〜４．５％）に止められてあり、この程度を越
えてｃｒを添加すると、炭化物が粗大化して靭性が低下
してしまう。
［発明が解決しようとする課題］
本発明の目的は、上記した技術の現状を打破し、使用条
件が苛酷な精密冷間加工用工具とくに各種金型の材料と
して好適な、焼入性にすぐれ、しかも高靭性を有する粉
末工具鋼、とくに粉末高速度工具鋼を提供することにあ
る。
［課題を解決するための手段］
本発明の粉末工具鋼は、Ｃ：Ｏ，ａ〜３．０％、Ｓｉ：
３．０％以下、Ｍｎ ：３．０％以下、Ｃｒ ：４．６
〜１０．０％、Ｗ：２０．０％以下、Ｖ二０．１〜５．
０％およびＣｏ：１０．０％以下を含有し、残余が実質
的にＦｅからなる合金組成の、焼入性および靭性にすぐ
れた粉末工具鋼である。
この鋼は、上記組成に加えて、Ｍｏ：１０．０％以下を
、Ｗ＋２Ｍｏ ＝Ｗｅｑ とするとき、５≦Ｗｅｑ≦
２０ の条件をみたすように含有してもよい。
上記いずれの合金組成の場合も、各成分の割合が、 ２
Ｍｏ／ＷｅＱ≦０．７ の条件および（または）、
０．０６Ｃｒ ＋０．０３３Ｗ＋０．０６３Ｍｏ ＋０
．２Ｖ＝Ｃｅｑとするとき、−０．２≦Ｃ−Ｃｅｑ≦０
．２ の条件をみたすことが好ましい。
［作 用］
発明者らは、高速度工具鋼の焼入性向上を意図して研究
の結果、ベイナイト開始点を遅くすることで焼入性が高
まること、それにはＣｒ含有量を増大させるのが最も効
果的であると推測した。
ところが、Ｃｒ量の増加はたしかにベイナイト開始点を
長時間側に移行させ、高さの向上には役立ったが、耐摩
耗性を担う一次品出炭化物が粗大になりやすく、靭性は
むしろ低下した。
この対策として、粉末冶金法を採用して完成したのが本
発明でおる。 粉末工具鋼においては、炭化物が均一微
細に晶出し、Ｃｒｉを高めて必要量の炭化物を、巨大晶
の生成を避けて確保することができる。
本発明の粉末工具鋼を形成する各成分元素の作用と組成
の限定理由を以下に記す。
Ｃ：Ｏ，ａ〜３．０％
多量の炭化物をつくるため、５ＫＨ５１のＣ含有量０．
８〜０．９％を下限とし、それより多い側にした。 こ
れにより、高い耐摩耗性を得るとともに、焼入性が高ま
る。 ３゜０％の上限に至ると、硬さ向上の効果が飽和
し靭性が低下する。
Ｓｉ：３．０％以下、Ｍｎ：３．０％以下ともに脱酸剤
として加える。 どちらも、多量に過ぎると靭性をそこ
なう。
Ｃｒ ：４．６〜１０．０％
多量のＣとともに炭化物を形成し、耐摩耗性と焼入性の
向上をもたらす。 ４．６％の下限は、前記したＳＫＨ
５１ｍのＣｒ量の上限４．５％を超える量であって、ベ
イナイト開始点を長時間側に移行させ、焼入れのときの
冷却速度が遅くても硬い鋼を与える。 一方、１０％の
上限を超える添加は、構成炭化物のバランスを悪くし、
靭性の低下を招く。
Ｗ：２０．０％以下
微細な炭化物ＷＣが析出して、耐摩耗性に寄与する。
多量になると、炭化物としてＷ２Ｃの割合が増えて焼入
性向上に役立たなくなるととともに、靭性にとってマイ
ナスになる。
Ｖ：０．１〜５．０％
微細な炭化物ＶＣを生成して、耐摩耗性を高める。 過
大になると靭性が低くなる。
Ｃｏ：１０．０％以下
耐熱性の向上に役立つほか、炭化物を生成して耐摩耗性
にも寄与する。 多量に加えると高価になるし、靭性を
低くする。
Ｍｏ：１０．０％以下（ただしＷ＋２Ｍｏ＝Ｗｅｑとし
たとき、５≦Ｗｅｑ≦２０＞
前記したように、Ｗの一部はＭｏで置き換えることがで
きる。 Ｍｏ添加の影響はＷの約半分で、多量の炭化物
Ｍｏ ＣおよびＭｏ２Ｃの生成は熱処理に不利益な存在
となるから、上記の制限を設けた。
ＭｏとＷの割合は、さらに上記Ｗｅｑに関して、２Ｍｏ
／Ｗｅ（１≦０．７の条件をみたすことが好ましい。
それによって、粉末工具鋼の靭性と硬さのバランスが実
用上好ましいものとなるからである。
本発明の粉末工具鋼をＷおよびＭｏの含有量に関して位
置づけると、添付図面のとおりでおる。
図の斜線を施した領域が本発明の合金組成の範囲である
。
靭性と硬さに対しては、ＷとＭｏのほかにＣｒとＶが大
きく影響する。
この観点から、
０．０６Ｃｒ ＋ ０．０３３Ｗ＋ ０．０６３Ｍｏ
＋ ０．２Ｖ＝Ｃｅｑとするとき、−０．２≦Ｃ−Ｃｅ
ｑ≦０．２ の条件をみたすように、各成分を配合する
ことが好ましい。
【実施例］
第１表に示す合金組成の鋼を溶製し、溶湯をガス噴霧に
より粉末化した。 これをＨＩＰにより焼結し、焼なま
しした状態で鍛造してから、焼入れ焼もどしの熱処理を
した。 焼入れは、真空加熱／ガス冷却により行なった
。冷却速度はおおよそ０．５℃／ ｓｅｃである。 一
方、焼戻しは工具使用時に達することのある温度を与え
て、高温焼戻しを採用した。
各供試材から試験片をつくり、靭性のめやすとして抗折
力を測定し、耐摩耗性と耐焼付性をしらべた。
耐摩耗性は大越式迅速摩耗試験により、下記の条件で実
施した。
相手材：３０Ｍ４１５（焼なまし）
辷り距離：２００ｍ
辷り速度： ２．９３ｍ／ｓｅｃ を荷 重：
５．３に９ｆ’
耐焼付性は、円柱状の供試材を軸を中心に回転させつつ
、被加工材のブロック２個でそれをはさみ、油圧により
ブロックを押しっけて、供試材の回転に要するトルクが
急激に増大した点の押圧力をもって焼付荷重とする方法
で測定した。
以上の結果を、熱処理条件とともに第２表に示す。
［発明の効果１
本発明の粉末工具鋼は、大型の工具に加工しても、焼入
性が高いから十分な硬さが得られる。
多量の炭化物の微細析出により、耐摩耗性が高く、靭性
も十分なレベルにある。 従ってこの発明は、高速度工
具ｍ製品を真空熱処理した場合にも、その性能が十分発
揮できるようにした技術であるということができる。
この工具鋼は、大型で精密さを要求され、しかも苛酷な
条件下に使用される冷間加工工具、たとえば鍛造金型、
圧延ロールの材料として好適である。As a material for cold working tools, cold working tool steel, typified by JIS 5KH51, has conventionally been used as ingot material. This steel has excellent wear resistance and relatively high toughness, making it a material suitable for cold precision machining molds. However, in recent years, there has been a trend toward larger and more precise cold working tools, such as an increase in demand for large cold forging dies and a growing desire to reduce the clearance of the rear die. Vacuum heat treatment has come into widespread use. In vacuum heat treatment, cooling is performed using gas, so the cooling rate cannot be increased, and there is also the problem of mass effect due to the increase in the size of the object to be treated, so that the quenching effect tends to be insufficient. For this reason, materials with high hardenability, wear resistance, and high toughness are required. 5KH51 cannot meet this demand because it lacks hardness and wear resistance, and its hardenability is also low. In 5KH51, the Cr content, which affects hardenability, is limited to about 4% (3.8 to 4.5%), and if Cr is added beyond this level, the carbides become coarse and the toughness decreases. Resulting in. [Problems to be Solved by the Invention] The purpose of the present invention is to break through the current state of the technology as described above, and to develop a material with excellent hardenability that is suitable as a material for precision cold working tools, particularly various molds, which are used under severe conditions. The object of the present invention is to provide a powder tool steel, particularly a powder high-speed tool steel, which has high toughness. [Means for Solving the Problems] The powder tool steel of the present invention contains C:O, a~3.0%, Si:
3.0% or less, Mn: 3.0% or less, Cr: 4.6
~10.0%, W: 20.0% or less, V2 0.1~5.
It is a powder tool steel having an alloy composition containing 0% Co and 10.0% or less Co, with the remainder substantially consisting of Fe, and has excellent hardenability and toughness. In addition to the above composition, this steel has Mo: 10.0% or less, and when W + 2Mo = Weq, 5≦Weq≦
It may be contained so as to satisfy the conditions of 20. In any of the above alloy compositions, the ratio of each component is 2
Condition of Mo/WeQ≦0.7 and/or, 0.06Cr +0.033W+0.063Mo +0
．． When 2V=Ceq, -0.2≦C-Ceq≦0
．． It is preferable that condition 2 is satisfied. [Function] As a result of research aimed at improving the hardenability of high-speed tool steel, the inventors found that hardenability was increased by delaying the starting point of bainite, which could be achieved by increasing the Cr content. was assumed to be the most effective. However, although the increase in the amount of Cr did shift the bainite starting point to the long-term side and was useful for improving the height, the primary product carbides responsible for wear resistance tended to become coarser, and the toughness actually decreased. As a countermeasure to this problem, the present invention has been completed by adopting a powder metallurgy method. In powder tool steel, carbides are uniformly and finely crystallized, Cri is increased, and the necessary amount of carbides can be secured while avoiding the formation of giant crystals. The effects of each component element forming the powder tool steel of the present invention and reasons for limiting the composition are described below. C: O, a ~ 3.0% In order to create a large amount of carbide, the C content of 5KH51 is 0.
The lower limit was set at 8% to 0.9%, and the amount was set higher than that. This provides high wear resistance and increases hardenability. When the upper limit of 3.0% is reached, the effect of improving hardness is saturated and toughness decreases. Both Si: 3.0% or less and Mn: 3.0% or less are added as deoxidizing agents. Excessive amounts of both impair toughness. Cr: 4.6-10.0% Forms carbides together with a large amount of C, improving wear resistance and hardenability. The lower limit of 4.6% is the SKH
This amount exceeds the upper limit of 4.5% of the Cr content of 51m, shifts the bainite starting point to the long time side, and provides a hard steel even if the cooling rate during quenching is slow. On the other hand, addition exceeding the upper limit of 10% will worsen the balance of constituent carbides,
This leads to a decrease in toughness. W: 20.0% or less Fine carbide WC precipitates and contributes to wear resistance.
If the amount is too large, the proportion of W2C as a carbide increases, making it useless for improving hardenability and having a negative effect on toughness. V: 0.1-5.0% Generates fine carbide VC to improve wear resistance. If it becomes too large, the toughness will decrease. Co: 10.0% or less Not only helps improve heat resistance, but also contributes to wear resistance by forming carbides. If added in large quantities, it becomes expensive and reduces toughness. Mo: 10.0% or less (however, when W+2Mo=Weq, 5≦Weq≦20> As mentioned above, a part of W can be replaced with Mo. The effect of Mo addition is about half that of W, The above limitations were set because the generation of large amounts of carbides MoC and Mo2C is disadvantageous to heat treatment.
/We (preferably satisfies the condition of 1≦0.7.
This is because the powder tool steel has a practically preferable balance between toughness and hardness. The powder tool steel of the present invention is positioned in terms of W and Mo contents as shown in the attached drawings. The shaded area in the figure is the range of the alloy composition of the present invention. In addition to W and Mo, Cr and V have a large influence on toughness and hardness. From this point of view, 0.06Cr + 0.033W + 0.063Mo
+0.2V=Ceq, -0.2≦C-Ce
It is preferable to mix each component so that the condition of q≦0.2 is satisfied. [Example] Steel having the alloy composition shown in Table 1 was melted, and the molten metal was pulverized by gas spraying. This was sintered by HIP, forged in an annealed state, and then heat-treated for quenching and tempering. Hardening was performed by vacuum heating/gas cooling. The cooling rate is approximately 0.5°C/sec. On the other hand, high-temperature tempering was adopted, giving the temperature that can be reached during tool use. Test pieces were made from each sample material, transverse rupture strength was measured as a measure of toughness, and wear resistance and seizure resistance were examined. Abrasion resistance was measured using the Ohkoshi rapid abrasion test under the following conditions. Mating material: 30M415 (annealed) Sliding distance: 200m Sliding speed: 2.93m/sec Load:
5.3 to 9f' Seizure resistance was measured by rotating a cylindrical specimen around an axis, sandwiching it between two workpiece blocks, and pushing the blocks away using hydraulic pressure. It was measured using a method in which the pressing force at the point where the torque required for rotation suddenly increased was taken as the seizure load. The above results are shown in Table 2 together with the heat treatment conditions. [Effect of the Invention 1] Even when the powder tool steel of the present invention is processed into a large tool, sufficient hardness can be obtained because of its high hardenability. Due to the large amount of finely precipitated carbides, it has high wear resistance and sufficient toughness. Therefore, this invention can be said to be a technology that allows high-speed tool m products to exhibit their full performance even when subjected to vacuum heat treatment. This tool steel is used for large cold working tools that require precision and are used under harsh conditions, such as forging dies.
It is suitable as a material for rolling rolls.
添付図面は、本発明の粉末工具鋼のＷとＭｏの含有量に
関して組成範囲を示すグラフである。
特許出願人 −２大同特殊鋼株式会社
代理人 弁理士 須 賀 総 夫
Ｍｏ （％）The accompanying drawing is a graph showing the composition range in terms of W and Mo content of the powder tool steel of the present invention. Patent Applicant -2 Daido Steel Co., Ltd. Agent Patent Attorney Souo Suga Mo (%)
Claims (1)
ｎ：３．０％以下、Ｃｒ：４．６〜１０．０％、Ｗ：２
０．０％以下、Ｖ：０．１〜５．０％およびＣｏ：１０
．０％以下を含有し、残余が実質的にＦｅからなる合金
組成の、焼入性および靭性にすぐれた粉末工具鋼。 （２）請求項１の合金組成に加えて、Ｍｏ：１０．０％
以下を、Ｗ＋２Ｍｏ＝Ｗｅｑとするとき、５≦Ｗｅｑ≦
２０の条件をみたすように含有する粉末工具鋼。 （３）２Ｍｏ／Ｗｅｑ≦０．７の条件および（または） ０．０６Ｃｒ＋０．０３３Ｗ＋０．０６３Ｍｏ＋０．２
Ｖ＝Ｃｅｑとするとき、−０．２≦Ｃ−Ｃｅｑ≦０．２
の条件をみたす合金組成の、請求項１または２の粉末工
具鋼。[Claims] (1) C: 0.8 to 3.0%, Si: 3.0% or less, M
n: 3.0% or less, Cr: 4.6 to 10.0%, W: 2
0.0% or less, V: 0.1-5.0% and Co: 10
．． A powder tool steel having an alloy composition containing 0% or less of Fe, with the remainder substantially consisting of Fe, and having excellent hardenability and toughness. (2) In addition to the alloy composition of claim 1, Mo: 10.0%
When the following is W+2Mo=Weq, 5≦Weq≦
Powder tool steel containing so as to satisfy the conditions of 20. (3) Condition of 2Mo/Weq≦0.7 and/or 0.06Cr+0.033W+0.063Mo+0.2
When V=Ceq, -0.2≦C-Ceq≦0.2
The powder tool steel according to claim 1 or 2, having an alloy composition that satisfies the following conditions.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP99389A JPH02182867A (en) | 1989-01-06 | 1989-01-06 | Powdered tool steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP99389A JPH02182867A (en) | 1989-01-06 | 1989-01-06 | Powdered tool steel |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02182867A true JPH02182867A (en) | 1990-07-17 |
Family
ID=11489122
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP99389A Pending JPH02182867A (en) | 1989-01-06 | 1989-01-06 | Powdered tool steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02182867A (en) |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4115842A1 (en) * | 1990-07-09 | 1992-01-16 | Venanzetti S R L | ALLOY FOR THE PRODUCTION OF A SPECIAL STEEL FOR TOOLS FOR COLD TREATMENT |
| JPH04221047A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH04221044A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH04221046A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH0543993A (en) * | 1990-12-19 | 1993-02-23 | Kubota Corp | High speed steel type sintered alloy |
| BE1011021A5 (en) * | 1996-01-16 | 1999-04-06 | Hitachi Powdered Metals | Source material sintered powder for wear-resistant. |
| JP2012067325A (en) * | 2010-09-21 | 2012-04-05 | Mitsubishi Materials Corp | Alloy steel having excellent high temperature tempering softening resistance |
| JP2012177172A (en) * | 2011-02-28 | 2012-09-13 | Mitsubishi Materials Corp | Alloy steel with superior resistance to high temperature temper softening |
| JP2015160957A (en) * | 2014-02-26 | 2015-09-07 | 山陽特殊製鋼株式会社 | Powder high speed tool steel excellent in abrasion resistance and manufacturing method therefor |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54116318A (en) * | 1978-03-01 | 1979-09-10 | Kobe Steel Ltd | Highly wear resistant powder high speed steel |
| JPS58185751A (en) * | 1982-04-21 | 1983-10-29 | Kobe Steel Ltd | High speed steel manufactured by powder metallurgy processing |
| JPS62120401A (en) * | 1985-11-20 | 1987-06-01 | Hitachi Metals Ltd | Production of sintered tool steel member |
| JPS6447836A (en) * | 1987-08-18 | 1989-02-22 | Kobe Steel Ltd | High hardness and high speed sintered steel ingot having excellent hot workability |
-
1989
- 1989-01-06 JP JP99389A patent/JPH02182867A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54116318A (en) * | 1978-03-01 | 1979-09-10 | Kobe Steel Ltd | Highly wear resistant powder high speed steel |
| JPS58185751A (en) * | 1982-04-21 | 1983-10-29 | Kobe Steel Ltd | High speed steel manufactured by powder metallurgy processing |
| JPS62120401A (en) * | 1985-11-20 | 1987-06-01 | Hitachi Metals Ltd | Production of sintered tool steel member |
| JPS6447836A (en) * | 1987-08-18 | 1989-02-22 | Kobe Steel Ltd | High hardness and high speed sintered steel ingot having excellent hot workability |
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE4115842A1 (en) * | 1990-07-09 | 1992-01-16 | Venanzetti S R L | ALLOY FOR THE PRODUCTION OF A SPECIAL STEEL FOR TOOLS FOR COLD TREATMENT |
| JPH04221047A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH04221044A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH04221046A (en) * | 1990-12-19 | 1992-08-11 | Kubota Corp | High speed steel type sintered alloy |
| JPH0543993A (en) * | 1990-12-19 | 1993-02-23 | Kubota Corp | High speed steel type sintered alloy |
| BE1011021A5 (en) * | 1996-01-16 | 1999-04-06 | Hitachi Powdered Metals | Source material sintered powder for wear-resistant. |
| JP2012067325A (en) * | 2010-09-21 | 2012-04-05 | Mitsubishi Materials Corp | Alloy steel having excellent high temperature tempering softening resistance |
| JP2012177172A (en) * | 2011-02-28 | 2012-09-13 | Mitsubishi Materials Corp | Alloy steel with superior resistance to high temperature temper softening |
| JP2015160957A (en) * | 2014-02-26 | 2015-09-07 | 山陽特殊製鋼株式会社 | Powder high speed tool steel excellent in abrasion resistance and manufacturing method therefor |
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