JPH07116548B2 - High hardness alloy steel manufacturing method - Google Patents
High hardness alloy steel manufacturing methodInfo
- Publication number
- JPH07116548B2 JPH07116548B2 JP1260068A JP26006889A JPH07116548B2 JP H07116548 B2 JPH07116548 B2 JP H07116548B2 JP 1260068 A JP1260068 A JP 1260068A JP 26006889 A JP26006889 A JP 26006889A JP H07116548 B2 JPH07116548 B2 JP H07116548B2
- Authority
- JP
- Japan
- Prior art keywords
- alloy
- alloy steel
- powder
- high hardness
- hardness
- 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
Description
【発明の詳細な説明】 〔産業上の利用分野〕 本発明は、焼結後の後加工性に優れつつ、最終的に表面
硬度がビッカース硬度Hv（10）で700を超える合金鋼が
得られる製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial field of application] The present invention provides an alloy steel having a Vickers hardness Hv (10) of more than 700 while having excellent post-workability after sintering. It relates to a manufacturing method.
三次元的に複雑な形状を有する製品を製造するため、純
Fe、Fe−Ni系合金、Fe−Ni−Ｃ系合金、ステンレス鋼、
析出硬化型ステンレス鋼、高速度鋼、超硬合金等の金属
粉末とバインダーを混練して得た混練物を射出成形し、
その後脱バインダーして焼結する射出成形粉末冶金法が
知られている。そしてこれらの合金は通常、焼結後、更
に、サイジング加工を始めとしてフライス加工、穴あけ
加工、タップ加工、バレル研磨など種々な後加工および
焼入れ焼戻し処理、軟化焼鈍、磁気焼鈍、時効処理、HI
P処理などの熱処理を経て製品となるが、これらの製品
には焼結上り状態で後加工性が良好で、それでいて焼入
れ焼戻し処理により表面が硬化し耐磨耗性が良好となる
ことが、広い利用分野で求められている。To produce products with three-dimensionally complex shapes,
Fe, Fe-Ni based alloy, Fe-Ni-C based alloy, stainless steel,
Precipitation hardening type stainless steel, high speed steel, cemented carbide and other metal powder and binder are kneaded to obtain a kneaded product, which is injection molded,
An injection molding powder metallurgical method in which the binder is then removed and sintered is known. These alloys are usually sintered, and then various sizing and other post-processing such as milling, drilling, tapping, barrel polishing, quenching and tempering, softening annealing, magnetic annealing, aging treatment, HI
Although they become products after heat treatment such as P treatment, these products have good post-workability in the ascended state, but the surface is hardened by quenching and tempering treatment and wear resistance is good. Required in the field of use.
前記合金の中でこのような特性を最も満たす材質とし
て、Fe−Ni−Ｃ合金が従来より使われてきた。Fe-Ni-C alloy has been conventionally used as a material that most satisfies such characteristics among the alloys.
〔発明が解決しようとする課題〕 しかるに、Fe−Ni−Ｃ合金は、焼結上り状態で後加工性
は良いものの、焼入性が十分でなく、油焼入および焼戻
しの熱処理をした後の硬化がビッカース硬度Hv（10）
（以下、単にHv（10）と記す）で700を超えることはな
く、耐磨耗性に今一歩優えなかった。かかる理由から本
発明の目的は、焼結上り状態にて後加工性がFe−Ni−Ｃ
合金と同等程度でありつつ、最終的に熱処理により表面
硬度がHv（10）700を超える合金鋼を製造する新規な方
法を提供することにある。[Problems to be Solved by the Invention] However, although the Fe-Ni-C alloy has good post-workability in the ascended state, it does not have sufficient hardenability, and it is Hardening is Vickers hardness Hv (10)
(Hereinafter, simply referred to as Hv (10)), it did not exceed 700, and the wear resistance was not superior. For this reason, the object of the present invention is to have a post-workability of Fe-Ni-C in the as-sintered state.
It is an object of the present invention to provide a novel method for producing an alloy steel having a surface hardness of more than Hv (10) 700 by heat treatment, which is equivalent to the alloy.
本発明は、上記の目的を達成するものとして、Cr0.5〜
1.0重量％、C0.5〜0.9重量％、残部Feからなる合金鋼の
製造方法であって、Fe−Cr合金粉末とカルボニルFe粉末
と黒鉛粉末とを上記組成の合金鋼が得られるように配合
し、射出成形法により得られた成形体を真空下1250℃で
焼結し、その後焼入れすることからなる、表面硬度がHv
（10）で700を超える合金鋼の製造方法を提供する。The present invention achieves the above-mentioned object by using Cr 0.5 to
A method for producing an alloy steel consisting of 1.0% by weight, C0.5 to 0.9% by weight, and the balance being Fe, wherein Fe-Cr alloy powder, carbonyl Fe powder, and graphite powder are compounded so as to obtain an alloy steel having the above composition. Then, the molded body obtained by the injection molding method is sintered at 1250 ° C. under vacuum and then quenched, and the surface hardness is Hv.
(10) provides a method for producing over 700 alloy steels.
本発明の製造方法に出発原料として用いるものを例示す
ると以下のものが挙げられるが、これに限定されるもの
でははい。Examples of the starting material used in the production method of the present invention include the following, but the present invention is not limited thereto.
Fe−Cr合金粉末としては、Fe−30重量％Cr合金の微粉末
が挙げられる。Examples of the Fe-Cr alloy powder include fine powder of Fe-30 wt% Cr alloy.
カルボニルFeとしては、カーボンを0.9重量％含有する
ものが例示される。Examples of carbonyl Fe include those containing 0.9% by weight of carbon.
黒鉛粉末としては、天然黒鉛の粉末が例示できる。Examples of the graphite powder include natural graphite powder.
射出成形の方法は、定法に従い、通常、原料粉末を所要
組成に配合し、有機バインダーを加えて混練し、得られ
た混練物を金型に射出成形し、次いでこうして得られた
成形体を脱バインダー後焼結することにより行われる。The injection molding is carried out according to a standard method, usually by mixing the raw material powder to the required composition, adding an organic binder and kneading, injection-molding the resulting kneaded product, and then removing the molded product thus obtained. It is performed by sintering after the binder.
焼結は真空下、1250℃で行われ、しかる後に焼入れが行
われる。こうして、Hv（10）700を超える合金鋼が得ら
れる。Sintering is performed under vacuum at 1250 ° C., followed by quenching. Thus, an alloy steel having a Hv (10) of more than 700 is obtained.
水アトマイズ法で作られたFe−30重量％Cr母合金微粉末
（平均粒径30μｍ）とカーボンを0.9重量％含有するカ
ーボニルFe粉末（平均粒径５μｍ）と天然黒鉛粉末（平
均粒径22μｍ）を表１に示す組成の合金が得られるよう
に配合し、有機バインダーを加えて各々10kg混練した。
この混練物を金型に射出成形して、幅10mm、厚み10mm、
長さ55mmのテストピースを得た（試験No.1〜６）。Fe-30 wt% Cr master alloy fine powder (average particle size 30 μm), carbonyl Fe powder (average particle size 5 μm) containing 0.9 wt% carbon and natural graphite powder (average particle size 22 μm) made by water atomization method Were blended so as to obtain an alloy having the composition shown in Table 1, an organic binder was added, and 10 kg of each was kneaded.
This kneaded product is injection-molded in a mold to have a width of 10 mm, a thickness of 10 mm,
Test pieces having a length of 55 mm were obtained (Test Nos. 1 to 6).
これらの成形体を窒素雰囲気中で300℃迄加熱して脱バ
インダーし、その後、半連続式真空焼結炉にて真空度５
×10-2Torr,焼結温度1250℃で健全な焼結体を得た。こ
れらの焼結体は各組成により若干異なるが93％から95％
の相対密度比を示していた。These molded bodies are heated to 300 ° C in a nitrogen atmosphere to remove the binder, and then the degree of vacuum is 5 in a semi-continuous vacuum sintering furnace.
A healthy sintered body was obtained at × 10 -2 Torr and a sintering temperature of 1250 ℃. The composition of these sintered bodies varies from 93% to 95% depending on the composition.
The relative density ratio of
次にこれらの焼結体のHv（10）を荷重10kgで測定した
後、油焼入れおよび焼戻し処理を施した。焼入条件は83
0℃で30分間保持後、油焼入れ、焼戻し条件は170℃で60
分間保持後、空冷とした。最後にこれらの熱処理体のHv
（10）を荷重10kgにて測定した。Next, after measuring Hv (10) of these sintered bodies under a load of 10 kg, oil quenching and tempering treatments were performed. Quenching condition is 83
After holding at 0 ℃ for 30 minutes, oil quenching and tempering conditions are 170 ℃ and 60
After holding for a minute, it was cooled with air. Finally, the Hv of these heat-treated bodies
(10) was measured with a load of 10 kg.
更に、カーボンを0.9重量％含有するカルボニルFe粉末
（平均粒径５μｍ）とカルボニルNi粉末（平均粒径７μ
ｍ）を表１に示す組成に配合した以外は前記と同様にし
て焼結体を得、Hv（10）を測定した（試験No.7）。な
お、この焼結体の相対密度比は95％であった。In addition, carbonyl Fe powder (average particle size 5 μm) containing 0.9% by weight of carbon and carbonyl Ni powder (average particle size 7 μm)
Hv (10) was measured in the same manner as described above except that m) was blended in the composition shown in Table 1 (Test No. 7). The relative density ratio of this sintered body was 95%.
以上の焼結体および熱処理体の硬度測定結果を表１に示
す。Table 1 shows the hardness measurement results of the above-described sintered body and heat-treated body.
この表から明らかなように本発明の方法により得られる
合金は焼結後焼入れ前の硬度がHv（10）で260以下と低
く、後加工性が従来合金と同程度である。それでいて、
熱処理後の硬度がHv（10）で700を超えることがわか
る。 As is clear from this table, the hardness of the alloy obtained by the method of the present invention after sintering and before quenching is as low as 260 or less in Hv (10), and the post-workability is about the same as the conventional alloy. Still,
It can be seen that the hardness after heat treatment exceeds 700 in Hv (10).
［発明の効果］ 本発明の方法により、焼結後の後加工性が従来のFe−Ni
−Ｃ合金と同等程度でありながら、最終的な焼入れおよ
び焼戻しの熱処理により表面硬度がHv（10）700を超え
る耐磨耗性に優れた高硬度合金鋼を得ることができる。EFFECTS OF THE INVENTION According to the method of the present invention, the post-workability after sintering is the same as that of conventional Fe-Ni
It is possible to obtain a high hardness alloy steel having a surface hardness exceeding Hv (10) 700 and having excellent wear resistance, which is about the same as that of the -C alloy but is subjected to final quenching and tempering heat treatment.
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２２Ｃ 38/18 (56)参考文献 特開 昭61−174354（ＪＰ，Ａ) 特開 昭53−30413（ＪＰ，Ａ) 特開 昭60−208453（ＪＰ，Ａ) 特開 昭62−37302（ＪＰ，Ａ) 特開 昭63−227751（ＪＰ，Ａ) 特公 昭49−40523（ＪＰ，Ｂ１) 特公 昭56−43298（ＪＰ，Ｂ２)─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Internal reference number FI technical display location C22C 38/18 (56) References JP-A 61-174354 (JP, A) JP-A 53- 30413 (JP, A) JP 60-208453 (JP, A) JP 62-37302 (JP, A) JP 63-227751 (JP, A) JP-B 49-40523 (JP, B1) Japanese Patent Publication Sho 56-43298 (JP, B2)
Claims (1)
部Feからなる合金鋼の製造方法であって、 Fe−Cr合金粉末とカルボニルFe粉末と黒鉛粉末とを上記
組成の合金鋼が得られるように配合し、射出成形法によ
り得られた成形体を真空下1250℃で焼結し、その後焼入
れすることからなる、表面硬度がビッカース硬度Hv（1
0）で700を超える高硬度合金鋼の製造方法。1. A method for producing an alloy steel comprising Cr 0.5 to 1.0% by weight, C 0.5 to 0.9% by weight, and the balance Fe, wherein Fe--Cr alloy powder, carbonyl Fe powder and graphite powder are contained in the above composition. Alloy steel is obtained so that the molded product obtained by the injection molding method is sintered at 1250 ° C. under vacuum and then quenched, and the surface hardness is Vickers hardness Hv (1
0) A method of manufacturing high hardness alloy steel with over 700.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1260068A JPH07116548B2 (en) | 1989-10-06 | 1989-10-06 | High hardness alloy steel manufacturing method |
| EP90310942A EP0421811B1 (en) | 1989-10-06 | 1990-10-05 | Alloy steel for use in injection molded sinterings produced by powder metallurgy |
| DE69024582T DE69024582T2 (en) | 1989-10-06 | 1990-10-05 | Steel alloy for use in injection-molded powder-metallurgically produced sintered bodies |
| US07/716,742 US5141554A (en) | 1989-10-06 | 1991-06-14 | Injection-molded sintered alloy steel product |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1260068A JPH07116548B2 (en) | 1989-10-06 | 1989-10-06 | High hardness alloy steel manufacturing method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH03122258A JPH03122258A (en) | 1991-05-24 |
| JPH07116548B2 true JPH07116548B2 (en) | 1995-12-13 |
Family
ID=17342865
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1260068A Expired - Lifetime JPH07116548B2 (en) | 1989-10-06 | 1989-10-06 | High hardness alloy steel manufacturing method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH07116548B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4332189B2 (en) | 2007-08-09 | 2009-09-16 | トヨタ自動車株式会社 | Inflator and vehicle airbag apparatus using the same |
| JP5090100B2 (en) | 2007-08-09 | 2012-12-05 | 豊田合成株式会社 | Inflator |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5330413A (en) * | 1976-09-02 | 1978-03-22 | Honda Motor Co Ltd | Method of producing ironnbased sintered alloy |
| JPS60208453A (en) * | 1984-03-30 | 1985-10-21 | Kawasaki Steel Corp | Steel powder for high-density sintered alloy |
| JPS61174354A (en) * | 1985-01-28 | 1986-08-06 | Toyota Motor Corp | Manufacture of copper-containing sintered alloy excellent in high-temperature wear resistance |
-
1989
- 1989-10-06 JP JP1260068A patent/JPH07116548B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH03122258A (en) | 1991-05-24 |
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