JP3343747B2 - Powdered high speed steel - Google Patents
Powdered high speed steelInfo
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- JP3343747B2 JP3343747B2 JP33808893A JP33808893A JP3343747B2 JP 3343747 B2 JP3343747 B2 JP 3343747B2 JP 33808893 A JP33808893 A JP 33808893A JP 33808893 A JP33808893 A JP 33808893A JP 3343747 B2 JP3343747 B2 JP 3343747B2
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- weight
- speed steel
- carbide
- type carbide
- powdered high
- Prior art date
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Description
【０００１】[0001]
【産業上の利用分野】本発明は粉末ハイス鋼に関し、更
に詳しくは、その粉末ハイス鋼を用いて製造した切削工
具や金型などは、耐摩耗生が優れていると同時に被研削
性も優れている粉末ハイス鋼に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to powdered high-speed steel, and more particularly, to cutting tools and dies manufactured using the powdered high-speed steel, which have excellent wear resistance and excellent grindability. Regarding powdered high-speed steel.
【０００２】[0002]
【従来の技術】切削工具や金型などは、最近、粉末冶金
法で製造される場合が多い。その場合、例えば、切削工
具は次のようにして製造されている。すなわち、まず、
所定粒径の例えば粉末ハイス鋼を所定形状のモールド内
に充填したのち粉末ハイス鋼を焼結して目的形状に近似
した形状の素材を製造する。ついで、焼なまし状態で荒
加工したのち、例えば真空焼入炉を用いて熱入れし、そ
の後、雰囲気炉によって焼戻しを行い硬度を高める。そ
して最後に、研削砥石で研削して目的形状にする。2. Description of the Related Art Recently, cutting tools and dies are often manufactured by powder metallurgy. In that case, for example, the cutting tool is manufactured as follows. That is, first,
After a powdered high-speed steel having a predetermined particle size, for example, is filled in a mold having a predetermined shape, the powdered high-speed steel is sintered to produce a material having a shape similar to a target shape. Next, after roughing in an annealed state, the material is heated by using, for example, a vacuum quenching furnace, and then tempered by an atmosphere furnace to increase hardness. And finally, it is ground with a grinding wheel to obtain the desired shape.
【０００３】この切削工具の場合、それ自体の使用目的
からすれば、被切削材との関係では耐摩耗性に優れてい
ることが要求される。そのことと同時に、上記製造工程
からも明らかなように、焼結品である素材それ自体は最
終工程で研削されるので被研削性に優れる材料であり、
また焼入れ性に優れる材料であることが要求される。こ
のような要求に対しては、原料である粉末ハイス鋼にお
ける炭化物総量を増加させることにより、高合金化を進
めるという処置が採られている。[0003] In the case of this cutting tool, it is required that the cutting tool has excellent wear resistance in relation to the material to be cut, in view of its intended use. At the same time, as is evident from the above manufacturing process, the material itself, which is a sintered product, is ground in the final process, so it is a material excellent in grindability,
It is also required that the material has excellent hardenability. In response to such demands, measures have been taken to increase the total amount of carbides in the powdered high-speed steel, which is the raw material, to promote high alloying.
【０００４】しかしながら、このような処置を施すと、
得られた粉末ハイス鋼の素材は確かに耐摩耗性は向上す
るが、他方では、硬度が高くなりすぎて、被研削性の劣
化という問題が派生する。そのため、目的形状の切削工
具を研削するに要する時間は長くなって生産性の低下を
招き、最終製品のコスト上昇が引き起こされる。[0004] However, when such a treatment is performed,
Although the obtained material of the powdered high-speed steel certainly improves the wear resistance, on the other hand, the hardness becomes too high, which causes a problem of deterioration in grindability. Therefore, the time required to grind the cutting tool having the desired shape becomes longer, which causes a decrease in productivity and raises the cost of the final product.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、従来の粉末
ハイス鋼における上記した問題を解決し、それを用いて
製造した製品の耐摩耗性が優れていると同時に被研削性
も優れていて、例えば、切削工具や金型などを粉末冶金
法で製造するときの原料として有用な粉末ハイス鋼の提
供を目的とする。SUMMARY OF THE INVENTION The present invention solves the above-mentioned problems in the conventional powdered high-speed steel, and a product manufactured using the same has excellent wear resistance and excellent grindability. For example, an object of the present invention is to provide a powdered high-speed steel that is useful as a raw material when a cutting tool, a mold, or the like is manufactured by a powder metallurgy method.
【０００６】[0006]
【課題を解決するための手段】ところで、粉末ハイス鋼
においては、その組織内に各種の炭化物が析出してい
る。それら炭化物のうち、ＶＣのようなＭＣ型炭化物と
（Ｆｅ，Ｗ，Ｍｏ)6ＣのようなＭ6 Ｃ型炭化物の大きさ
と硬さが、そのハイス鋼の被研削性に影響を与えること
が知られている。By the way, in powdered high-speed steel, various carbides are precipitated in its structure. Among these carbides, the size and hardness of MC type carbide such as VC and M 6 C type carbide such as (Fe, W, Mo) 6 C may affect the grindability of the high-speed steel. Are known.
【０００７】そこで、本発明者は、硬度や抗折力が従来
からの粉末ハイス鋼と同等である鋼種において、炭化物
の種類と量がその鋼種の耐摩耗性と被研削性に及ぼす影
響を調査した。その結果、ＭＣ型炭化物とＭ6 Ｃ型炭化
物の総量と相互の存在比率が所定の範囲にある粉末ハイ
ス鋼は、焼入れ性はＪＩＳ ＳＫＨ５１とほぼ同等であ
り、硬度や抗折力も従来の粉末ハイス鋼と同等である
が、耐摩耗性と被研削性はいずれも従来の粉末ハイス鋼
に比べて優れているとの事実を見出し、本発明の粉末ハ
イス鋼を開発するに至った。Accordingly, the present inventors investigated the effect of the type and amount of carbide on the wear resistance and grindability of a steel type having the same hardness and bending strength as conventional powdered high-speed steel. did. As a result, the powdered high-speed steel in which the total amount of the MC type carbide and the M 6 C type carbide and the mutual abundance are within a predetermined range has almost the same hardenability as JIS SKH51, and the hardness and the bending strength are the same as those of the conventional powdered high-speed steel. Although it was equivalent to steel, it was found that both wear resistance and grindability were superior to conventional powdered high-speed steel, and the powdered high-speed steel of the present invention was developed.
【０００８】すなわち、本発明の粉末ハイス鋼は、Ｃ：
1.５〜2.５重量％，Ｓｉ：0.１〜1.０重量％，Ｍｎ：1.
０重量％以下，Ｃｒ：3.０〜6.０重量％，Ｍｏ：2.０〜
8.０重量％，Ｗ：5.０〜２0.０重量％，Ｖ：6.０〜１0.
０重量％，Ｃｏ：2.０重量％以下，残部がＦｅから成
り、ＭＣ型炭化物とＭ6 Ｃ型炭化物の炭化物体積率をそ
れぞれａ体積％，ｂ体積％としたとき、ａ，ｂの間で
は、次式：１５≦ａ＋ｂ≦３０，0.７≦ａ／（ａ＋ｂ）
≦1.０の関係が成立していることを特徴とする。That is, the powdered high-speed steel of the present invention comprises:
1.5 to 2.5% by weight, Si: 0.1 to 1.0% by weight, Mn: 1.
0% by weight or less, Cr: 3.0 to 6.0% by weight, Mo: 2.0 to 2.0%
8.0% by weight, W: 5.0 to 20.0% by weight, V: 6.0 to 10%.
0% by weight, Co: 2.0% by weight or less, the balance being Fe, and when the carbide volume fractions of MC type carbide and M 6 C type carbide are a volume% and b volume%, respectively, between a and b Then, the following equation: 15 ≦ a + b ≦ 30, 0.7 ≦ a / (a + b)
It is characterized in that a relationship of ≦ 1.0 is established.
【０００９】この粉末ハイス鋼において、組織内に析出
している炭化物は、ＶＣを主体とするＭＣ型炭化物とＭ
6 Ｃや（Ｆｅ，Ｗ，Ｍｏ)6Ｃを主体とするＭ6 Ｃ型炭化
物になっている。これら炭化物のうち、ＭＣ型炭化物は
材料の耐摩耗性を向上させる働きをする。組織内で占有
するこれらＭＣ型炭化物とＭ6 Ｃ型炭化物の体積の割合
（炭化物体積率：体積％）をそれぞれａ，ｂとしたと
き、本発明の粉末ハイス鋼においては、ａ，ｂ間で、１
５≦ａ＋ｂ≦３０，0.７≦ａ／（ａ＋ｂ）≦1.０の関係
が成立している。[0009] In this powdered high-speed steel, carbides precipitated in the structure are MC-type carbides mainly composed of VC and M-type carbides.
It is an M 6 C-type carbide mainly composed of 6 C and (Fe, W, Mo) 6 C. Among these carbides, MC-type carbides function to improve the wear resistance of the material. Assuming that the ratio of the volume of the MC type carbide and the volume of the M 6 C type carbide occupying in the structure (carbide volume ratio: volume%) is a and b, respectively, in the powdered high-speed steel of the present invention, , 1
The relationship of 5 ≦ a + b ≦ 30, 0.7 ≦ a / (a + b) ≦ 1.0 holds.
【００１０】ここで、（ａ＋ｂ）は析出している炭化物
の総量を示す指標であり、この値が１５より小さい値と
なるような場合、すなわち、ＭＣ型炭化物とＭ6 Ｃ型炭
化物の総量が１５体積％より少ない場合には、従来の粉
末ハイス鋼に期待されるような耐摩耗性と被研削性の均
衡した性能向上が得られない。（ａ＋ｂ）が３０より大
きい値になるような場合、すなわち、炭化物総量が３０
体積％より多い場合には、そのような組織のハイス鋼を
工業的な規模で量産することがかなり困難になり、製造
コストの上昇が引き起こされる。Here, (a + b) is an index indicating the total amount of precipitated carbide. When this value is smaller than 15, that is, when the total amount of MC type carbide and M 6 C type carbide is If the content is less than 15% by volume, it is not possible to obtain a balanced improvement in wear resistance and grindability expected from conventional powdered high-speed steel. When (a + b) becomes a value larger than 30, that is, when the total amount of carbides is 30
If the content is higher than the volume percentage, mass production of such a structure of high-speed steel on an industrial scale becomes considerably difficult, and the production cost is increased.
【００１１】このようなことから、炭化物総量を表す
（ａ＋ｂ）は、１５〜３０体積％の範囲内に設定され
る。好ましくは、１５〜２５体積％にする。一方、ａ／
（ａ＋ｂ）は、組織内に析出している炭化物のうち、耐
摩耗性の向上に寄与するＭＣ型炭化物の存在割合を示す
指標であり、この値が大きくなるほど、ハイス鋼の耐摩
耗性は向上する。炭化物を全てＭＣ型炭化物にすること
は、耐摩耗性の向上という点で好ましいので、ａ／（ａ
＋ｂ）の値は、1.０を上限とする。From the above, (a + b) representing the total amount of carbides is set in the range of 15 to 30% by volume. Preferably, it is 15 to 25% by volume. On the other hand, a /
(A + b) is an index indicating the abundance ratio of MC type carbide which contributes to the improvement of wear resistance among the carbides precipitated in the structure, and the wear resistance of the high-speed steel increases as the value increases. I do. Since it is preferable that all carbides be MC-type carbides in terms of improvement of wear resistance, a / (a
+ B) has an upper limit of 1.0.
【００１２】また、ａ／（ａ＋ｂ）を0.７より小さくす
ると、ＭＣ型炭化物の耐摩耗性の向上効果が充分に発揮
されなくなり、得られたハイス鋼の耐摩耗性は不充分で
ある。ａ／（ａ＋ｂ）の好ましい値は、0.８〜1.０であ
る。また、上記したＭＣ型炭化物，Ｍ6 Ｃ型炭化物は、
その円相当粒径が、平均値で0.８μｍ以上であり、かつ
最大値が２〜８μｍになっていることが好ましい。On the other hand, if a / (a + b) is smaller than 0.7, the effect of improving the wear resistance of the MC type carbide is not sufficiently exhibited, and the wear resistance of the obtained high-speed steel is insufficient. The preferred value of a / (a + b) is 0.8 to 1.0. Further, the MC type carbide and the M 6 C type carbide described above are:
It is preferable that the equivalent circle diameter is 0.8 μm or more on average and the maximum value is 2 to 8 μm.
【００１３】円相当粒径を上記範囲に限定した理由は、
その平均値が0.８μｍより小さいと、鋼の被研削性は向
上するが、しかし耐摩耗性が低下する傾向を示す。他
方、最大炭化物の粒径が大きいほど耐摩耗性は向上する
が、８μｍを超える大きさになると、粉末ハイス鋼の特
徴である被研削性の良さが損なわれる。したがって、粉
末ハイス鋼としての特徴を損なわず、かつ耐摩耗性の低
下を防ぐために、最大炭化物の粒径としては２〜８μｍ
に調整することが好ましい。The reason for limiting the circle equivalent particle size to the above range is as follows.
When the average value is less than 0.8 μm, the grindability of the steel is improved, but the abrasion resistance tends to decrease. On the other hand, the larger the particle size of the largest carbide, the better the wear resistance. However, if the size exceeds 8 μm, the good grindability characteristic of powdered high-speed steel is impaired. Therefore, in order not to impair the characteristics of the powdered high-speed steel and to prevent a decrease in wear resistance, the maximum carbide particle size is 2 to 8 μm.
It is preferable to adjust to.
【００１４】炭化物の粒径調整は、鋼の製造時におい
て、溶鋼のソーキング温度やソーキング時間を適切に選
定することによって行うことができる。本発明の粉末ハ
イス鋼において、まず、Ｃは、主要にはＶと反応してＶ
Ｃを主体とするＭＣ型炭化物を生成させ、また、ＷやＭ
ｏと反応してＷ6 ＣやＭｏ6 Ｃを主体とするＭ6 Ｃ型炭
化物を生成させるための必須成分である。The grain size of the carbide can be adjusted by appropriately selecting the soaking temperature and soaking time of molten steel during the production of steel. In the powdered high-speed steel of the present invention, first, C mainly reacts with V to produce V
MC type carbide mainly composed of C, and W and M
It is an essential component for producing M 6 C-type carbide mainly composed of W 6 C and Mo 6 C by reacting with o.
【００１５】このときのＣの含有量は、計算上は、例え
ば、Ｇ．ＳＴＥＶＥＮらによって報告されている次式： ΔＣ＝Ｃ−（0.０６Ｃｒ＋0.０６３Ｍｏ＋0.０３３Ｗ＋
0.２Ｖ） におけるΔＣ値が−0.３〜0.１の範囲内になるような値
として設定される。具体的には、1.５〜2.５重量％に設
定される。The content of C at this time is calculated, for example, as follows: The following formula reported by STEVEN et al: ΔC = C− (0.06Cr + 0.063Mo + 0.033W +
0.2V) is set as a value such that the ΔC value falls within the range of -0.3 to 0.1. Specifically, it is set to 1.5 to 2.5% by weight.
【００１６】この含有量が1.５重量％より少なくなる
と、所定量のＭＣ型炭化物とＭ6 Ｃ型炭化物が生成され
ず、また2.５重量％より多くなると、マトリックス中の
Ｃ量が過剰となり靱性が損なわれる。Ｓｉは、溶製時に
おける脱酸剤として機能する成分であり、その含有量
は、通常のハイス鋼と同じように、0.１〜1.０重量％に
設定される。When the content is less than 1.5% by weight, predetermined amounts of MC type carbide and M 6 C type carbide are not formed, and when the content is more than 2.5% by weight, the amount of C in the matrix becomes excessive. And the toughness is impaired. Si is a component that functions as a deoxidizing agent at the time of smelting, and its content is set to 0.1 to 1.0% by weight, similarly to ordinary high-speed steel.
【００１７】Ｍｎも、Ｓｉと同じように脱酸剤として機
能する成分であり、その含有量は1.０重量％以下に設定
される。この含有量が1.０重量％より多い場合は、組織
内に残留オーステナイトが生成して全体は脆性となり、
切削工具などの材料として不適当になる。Ｃｒは焼入れ
性の向上に資する成分であり、その含有量は3.０〜6.０
重量％に設定される。Mn is also a component that functions as a deoxidizing agent like Si, and its content is set to 1.0% by weight or less. When this content is more than 1.0% by weight, residual austenite is generated in the structure and the whole becomes brittle,
It becomes unsuitable as a material for cutting tools. Cr is a component contributing to the improvement of hardenability, and its content is 3.0 to 6.0.
Set to% by weight.
【００１８】この含有量が3.０重量％より少ない場合
は、材料への焼入れが不充分になって硬度の向上が期待
できなくなる。また、6.０重量％よりも多くすると、Ｃ
ｒ2 Ｃ 3 のようなＣｒ系炭化物も生成して、目的とする
ＭＣ型炭化物とＭ6 Ｃ型炭化物の適正な生成が阻害され
るようになる。ＭｏはＭ6 Ｃ型炭化物を生成させるため
の必須成分であると同時に、そのＭｏ 6 Ｃが焼入れ時に
マトリックスに固溶することにより材料の２次硬化に資
する成分であり、その含有量は2.０〜8.０重量％に設定
される。When the content is less than 3.0% by weight
Is expected to improve hardness due to insufficient quenching of the material
become unable. If the content is more than 6.0% by weight, C
rTwoC ThreeAlso produces Cr-based carbides such as
MC type carbide and M6Proper formation of C-type carbides is hindered
Become so. Mo is M6To form C-type carbide
Is the essential component of 6C is hardened
Contributes to secondary hardening of material by solid solution in matrix
The content is set to 2.0-8.0% by weight
Is done.
【００１９】この含有量が2.０重量％にりも少なくする
と、上記した働きのうち、２次硬化作用が充分に発揮さ
れなくなり、また、8.０重量％よりも多くすると、Ｍｏ
6 Ｃの生成量が増加して、耐摩耗性の向上に寄与するＭ
Ｃ型炭化物の生成量の減少を招くようになる。Ｗは、上
記したＭｏの２倍量をもってＭｏと同じような働きをす
る成分であり、その含有量は5.０〜２０重量％に設定さ
れる。If the content is as low as 2.0% by weight, the secondary curing effect of the above functions will not be sufficiently exhibited, and if the content is more than 8.0% by weight, Mo will not be obtained.
The amount of 6 C generated increases, and M contributes to the improvement of wear resistance.
This leads to a reduction in the amount of C-type carbide produced. W is a component that functions in the same manner as Mo with twice the amount of Mo described above, and its content is set to 5.0 to 20% by weight.
【００２０】この含有量が5.０重量％より少ない場合
は、Ｍｏの場合と同じように、２次硬化作用が充分に発
揮されず、また２0.０重量％よりも多くすると、初期に
形成されるＭ6 Ｃ型炭化物の量が多くなり、総炭化物量
（ＭＣ＋Ｍ6 Ｃ）の増加により加工性が劣化する。Ｖは
ＶＣを主体とするＭＣ型炭化物を生成させるための必須
成分であり、その含有量は5.０〜１0.０重量％に設定さ
れる。When the content is less than 5.0% by weight, the secondary curing effect is not sufficiently exhibited as in the case of Mo. When the content is more than 20.0% by weight, the initial curing is not performed. The amount of M 6 C-type carbide to be used increases, and the workability deteriorates due to an increase in the total amount of carbide (MC + M 6 C). V is an essential component for producing MC-type carbide mainly composed of VC, and its content is set to 5.0 to 10.0% by weight.
【００２１】この含有量を5.０重量％より少なくする
と、前記したａ／（ａ＋ｂ）値は0.７にならない。ま
た、含有量を１0.０重量％にすると、ａ／（ａ＋ｂ）値
が1.０になる、すなわち、生成する炭化物が全てＭＣ型
炭化物になるので、Ｖの含有量は上記した範囲にする。
好ましくは、6.０〜１0.０重量％にする。Ｃｏは、材料
の硬度を高めたり、マトリクスの強度を高めたりする働
きをするが、他方では、ベーナイト変態開始時間を短時
間側にシフトさせて焼入れ性に大きな影響を与える成分
である。If the content is less than 5.0% by weight, the value of a / (a + b) will not be 0.7. Further, when the content is 10.0% by weight, the a / (a + b) value becomes 1.0, that is, since the generated carbides are all MC-type carbides, the V content is in the above range. .
Preferably, the content is 6.0 to 10.0% by weight. Co functions to increase the hardness of the material and the strength of the matrix, but on the other hand, is a component that shifts the bainite transformation start time to a shorter time side and greatly affects the hardenability.
【００２２】したがって、焼入れ性をＪＩＳ ＳＫＨ５
１と同等にすることを目的とする場合には、材料にＣｏ
を含有させないことが好ましいことになる。しかしなが
ら、鋼の溶製時に、使用スクラップなど系外から混入す
ることはさけられないが、そのことを前提とした場合で
あっても、ハイス鋼の耐摩耗性と被研削性を確保するた
めには、Ｃｏの含有量は2.０重量％を上限とする。Therefore, the hardenability is determined according to JIS SKH5.
In the case where the purpose is to make it equal to 1, Co
Is preferably not contained. However, when melting steel, it is inevitable to mix it from outside the system such as scraps used, but even on the premise of this, in order to ensure the wear resistance and grindability of high-speed steel. The upper limit of the content of Co is 2.0% by weight.
【００２３】本発明の粉末ハイス鋼は、上記した各成分
の所定量から成る合金を溶製し、ガス噴霧後、ＨＩＰ缶
充填，ＨＩＰ処理を行い、炭化物の粒径を大きくするた
めの拡散処理を行ったのち、熱間鍛造して所定の素材に
する。The powdered high-speed steel of the present invention is prepared by melting an alloy consisting of a predetermined amount of each of the above-mentioned components, performing gas spraying, filling the HIP can, performing HIP treatment, and performing a diffusion treatment for increasing the particle size of the carbide. After that, hot forging is performed to obtain a predetermined material.
【００２４】[0024]
実施例１〜１３，比較例１〜１３ 表１で示した各種組成の鋼を溶製した。 Examples 1 to 13 and Comparative Examples 1 to 13 Steels of various compositions shown in Table 1 were melted.
【００２５】[0025]
【表１】 [Table 1]
【００２６】これらの鋼につき、温度１１００℃，減面
率５０％以上の熱間鍛造を行い、焼鈍して供試材にし
た。これら各供試材については、焼鈍後の状態における
硬度（ＨＲＣ）を測定した。その結果を表２，３に示し
た。その後、各鋼に、１１６０〜１２００℃の温度域で
真空焼入れを行い、５２０〜５６０℃の温度域で１hr×
３回の焼戻しを行い、そのときの硬度（ＨＲＣ），抗折
力，耐摩耗性，研削性，炭化物分布を測定した。その結
果も表２，３に示した。Each of these steels was subjected to hot forging at a temperature of 1100 ° C. and a reduction of area of 50% or more, and annealed to obtain a test material. For each of these test materials, the hardness (HRC) in the state after annealing was measured. The results are shown in Tables 2 and 3. Thereafter, each steel is subjected to vacuum quenching in a temperature range of 1160 to 1200 ° C., and a temperature of 520 to 560 ° C. for 1 hour ×
The tempering was performed three times, and the hardness (HRC), bending strength, wear resistance, grindability, and carbide distribution at that time were measured. The results are also shown in Tables 2 and 3.
【００２７】炭化物体積率（ａ）と円相当粒径の測定：
Ｃｒ3 Ｏ3 電解腐食した試料を使用し、倍率２０００倍
でＳＥＭ写真を撮影したのち、ルーゼックスイメージア
ナライザーで面積率（ａ）（＝体積率）として測定。な
お、円相当粒径は、異形形状の炭化物を円相当粒径に
し、その平均値を求めた。Measurement of carbide volume fraction (a) and equivalent circle particle size:
Using a sample subjected to electrolytic corrosion of Cr 3 O 3 , a SEM photograph was taken at a magnification of 2000 times, and measured as an area ratio (a) (= volume ratio) with a Luzex image analyzer. The circle equivalent particle diameter was obtained by changing the irregular shaped carbide to a circle equivalent particle diameter and calculating the average value.
【００２８】炭化物体積率（ｂ）と円相当粒径の測定：
腐食液としてＫＭｎＯ4 を用いて腐食したことを除いて
は、炭化物体積率（ａ）と円相当粒径の測定と同じ。ま
た、上記各鋼につき、下記の仕様で耐摩耗性指数と研削
性指数を算出した。 耐摩耗性指数：大越式摩耗試験法を適用し、比較例１の
結果を１００としたときの相対値として表示。この値が
大きい材料ほど耐摩耗性が優れていることを表す。 研削性指数：研磨砥石としてレジンボンド砥石を用い、
比較例１の結果を１００としたときの相対値として表
示。この値が大きい材料ほど被研削性が優れていること
を表す。 以上の結果を一括して表２，３に示した。なお、表２，
３では、各鋼について算出されるΔＣ値も併記した。Measurement of carbide volume fraction (b) and equivalent circle particle size:
Except for corrosion using KMnO 4 as a corrosive liquid, the same as the measurement of the carbide volume fraction (a) and the circle equivalent particle size. The wear resistance index and the grindability index were calculated for each of the above steels according to the following specifications. Abrasion resistance index: Applied by the Ogoshi abrasion test method and expressed as a relative value when the result of Comparative Example 1 is set to 100. A material having a larger value indicates better wear resistance. Grindability index: Using a resin bond whetstone as the polishing whetstone,
Displayed as a relative value when the result of Comparative Example 1 is set to 100. A material having a larger value indicates better grindability. The above results are collectively shown in Tables 2 and 3. Table 2,
In No. 3, the ΔC value calculated for each steel is also shown.
【００２９】[0029]
【表２】 [Table 2]
【００３０】[0030]
【表３】 [Table 3]
【００３１】表２，３において、従来のハイス鋼である
比較例１と本発明のハイス鋼である実施例１０を比較す
れば明らかなように、両者の炭化物総量（ａ＋ｂ）と焼
入れ後の硬さはほぼ同等であるが、ＭＣ型炭化物の体積
率（ａ）が約２倍値になっている実施例１は、比較例１
に対し、その耐摩耗性指数が２０％上昇し、かつ研削性
指数が９０％以上大きい値になっていて、耐摩耗性と被
研削性のいずれもが優れている。In Tables 2 and 3, as is clear from comparison between Comparative Example 1 which is a conventional high-speed steel and Example 10 which is a high-speed steel of the present invention, the total amount of carbide (a + b) and the hardness after quenching are high. Example 1 in which the volume ratio (a) of the MC type carbide is about twice as large as Comparative Example 1
On the other hand, the wear resistance index increased by 20% and the grindability index increased by 90% or more, and both the wear resistance and the grindability were excellent.
【００３２】[0032]
【発明の効果】以上の説明で明らかなように、本発明の
粉末ハイス鋼は、耐摩耗性が優れていると同時に被研削
性も優れている。しかも、焼入れ後の硬度は、従来のハ
イス鋼とほぼ同等である。これは、炭化物総量を増加さ
せ、その炭化物総量におけるＭＣ型炭化物の割合を高め
たことがもたらす効果である。As is apparent from the above description, the powdered high-speed steel of the present invention has excellent wear resistance and excellent grindability. Moreover, the hardness after quenching is almost equal to that of the conventional high-speed steel. This is an effect brought about by increasing the total amount of carbides and increasing the proportion of MC-type carbides in the total amount of carbides.
【００３３】したがって、本発明の粉末ハイス鋼は、粉
末冶金法で製造する切削工具や金型の原料素材としてそ
の工業的価値は大である。Therefore, the powdered high-speed steel of the present invention has great industrial value as a raw material for cutting tools and dies manufactured by powder metallurgy.
Claims (3)
０重量％，Ｍｎ：1.０重量％以下，Ｃｒ：3.０〜6.０重
量％，Ｍｏ：2.０〜8.０重量％，Ｗ：5.０〜２0.０重量
％，Ｖ：5.０〜１0.０重量％，Ｃｏ：2.０重量％以下，
残部がＦｅから成り、ＭＣ型炭化物とＭ6 Ｃ型炭化物の
炭化物体積率をそれぞれａ体積％，ｂ体積％としたと
き、ａ，ｂの間では、次式：１５≦ａ＋ｂ≦３０，0.７
≦ａ／（ａ＋ｂ）≦1.０の関係が成立していることを特
徴とする粉末ハイス鋼。1. C: 1.5 to 2.5% by weight, Si: 0.1 to 1.1%.
0% by weight, Mn: 1.0% by weight or less, Cr: 3.0 to 6.0% by weight, Mo: 2.0 to 8.0% by weight, W: 5.0 to 20.0% by weight, V : 5.0 to 10.0% by weight, Co: 2.0% by weight or less,
When the balance is made of Fe and the carbide volume ratios of the MC type carbide and the M 6 C type carbide are a volume% and b volume%, respectively, between a and b, the following formula: 15 ≦ a + b ≦ 30,0. 7
A powdered high-speed steel characterized by satisfying a relationship of ≦ a / (a + b) ≦ 1.0.
相当平均粒径が0.８μｍ以上であり、かつ円相当最大粒
径が２〜８μｍである請求項１の粉末ハイス鋼。2. The powdered high-speed steel according to claim 1, wherein the MC-type carbide and the M 6 C-type carbide have a circle-equivalent average particle size of 0.8 μm or more and a circle-equivalent maximum particle size of 2 to 8 μm.
０重量％，Ｍｎ：1.０重量％以下，Ｃｒ：3.０〜6.０重
量％，Ｍｏ：2.０〜8.０重量％，Ｗ：5.０〜１5.０重量
％，Ｖ：6.０〜１0.０重量％，Ｃｏ：2.０重量％，残部
がＦｅから成り、ＭＣ型炭化物の体積率ａ（％）とＭ6
Ｃ型炭化物の体積率ｂ（％）の間では、１５≦ａ＋ｂ≦
２５，0.８≦ａ／（ａ＋ｂ）≦1.０の関係が成立してお
り、前記ＭＣ型炭化物と前記Ｍ6 Ｃ型炭化物の円相当平
均粒径が0.８μｍ以上で、かつ、円相当最大粒径が２〜
８μｍである請求項１の粉末ハイス鋼。3. C: 1.5-2.5% by weight, Si: 0.1-1.0%.
0% by weight, Mn: 1.0% by weight or less, Cr: 3.0 to 6.0% by weight, Mo: 2.0 to 8.0% by weight, W: 5.0 to 15.0% by weight, V : 6.0 to 10.0% by weight, Co: 2.0% by weight, the balance being Fe, the volume fraction a (%) of MC type carbide and M 6
Between the volume fractions b (%) of the C-type carbide, 15 ≦ a + b ≦
A relationship of 25, 0.8 ≦ a / (a + b) ≦ 1.0 is satisfied, and the MC-type carbide and the M 6 C-type carbide have a circle-equivalent average particle diameter of 0.8 μm or more, and The equivalent maximum particle size is 2
The powdered high-speed steel according to claim 1, which is 8 µm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33808893A JP3343747B2 (en) | 1993-12-28 | 1993-12-28 | Powdered high speed steel |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP33808893A JP3343747B2 (en) | 1993-12-28 | 1993-12-28 | Powdered high speed steel |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH07188859A JPH07188859A (en) | 1995-07-25 |
| JP3343747B2 true JP3343747B2 (en) | 2002-11-11 |
Family
ID=18314795
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP33808893A Expired - Fee Related JP3343747B2 (en) | 1993-12-28 | 1993-12-28 | Powdered high speed steel |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3343747B2 (en) |
Families Citing this family (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4737606B2 (en) * | 2004-11-18 | 2011-08-03 | 日立金属株式会社 | Cold die steel with excellent deformation suppression characteristics and galling resistance |
| JP5561601B2 (en) * | 2010-03-25 | 2014-07-30 | 日立金属株式会社 | Steel cutting method |
| CN102909372B (en) * | 2011-08-03 | 2015-03-18 | 东睦新材料集团股份有限公司 | Manufacturing method for valve plate of compressor |
| JP6516440B2 (en) * | 2013-11-27 | 2019-05-22 | 山陽特殊製鋼株式会社 | Powdered high speed tool steel |
| EP2933345A1 (en) | 2014-04-14 | 2015-10-21 | Uddeholms AB | Cold work tool steel |
| CN110273097B (en) * | 2019-06-28 | 2021-02-23 | 鞍钢股份有限公司 | VC/V10 powder high-speed steel composite material and preparation method thereof |
| CN117564281B (en) * | 2024-01-15 | 2024-04-05 | 西安欧中材料科技股份有限公司 | Preparation method of low-oxygen increment high-carbon high-alloy high-speed steel powder |
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1993
- 1993-12-28 JP JP33808893A patent/JP3343747B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JPH07188859A (en) | 1995-07-25 |
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