JPH06336636A - Production of austenitic-ferritic stainless steel having ultrafine-grained structure - Google Patents
Production of austenitic-ferritic stainless steel having ultrafine-grained structureInfo
- Publication number
- JPH06336636A JPH06336636A JP5151213A JP15121393A JPH06336636A JP H06336636 A JPH06336636 A JP H06336636A JP 5151213 A JP5151213 A JP 5151213A JP 15121393 A JP15121393 A JP 15121393A JP H06336636 A JPH06336636 A JP H06336636A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- powder
- austenite
- ferrite
- phase
- 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
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 29
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 17
- 239000000843 powder Substances 0.000 claims abstract description 44
- 229910000859 α-Fe Inorganic materials 0.000 claims abstract description 30
- 229910001566 austenite Inorganic materials 0.000 claims abstract description 20
- 238000005551 mechanical alloying Methods 0.000 claims abstract description 15
- 239000006104 solid solution Substances 0.000 claims abstract description 11
- 238000010438 heat treatment Methods 0.000 claims abstract description 10
- 239000010935 stainless steel Substances 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims description 9
- 238000007711 solidification Methods 0.000 claims description 6
- 230000008023 solidification Effects 0.000 claims description 6
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 238000012545 processing Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 238000001513 hot isostatic pressing Methods 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 238000007731 hot pressing Methods 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 239000013535 sea water Substances 0.000 description 2
- 230000000930 thermomechanical effect Effects 0.000 description 2
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 238000002441 X-ray diffraction Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 1
- 239000002775 capsule Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- -1 for example Inorganic materials 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Powder Metallurgy (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は超微細粒組織を有するオ
ーステナイト・フェライト系ステンレス鋼の製造方法に
関し、さらに詳しくは、海洋構造物に適合する機械的性
質を向上させることができる超微細粒組織を有するオー
ステナイト・フェライト系ステンレス鋼の製造方法に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an austenitic ferritic stainless steel having an ultrafine grain structure, and more specifically, an ultrafine grain structure capable of improving mechanical properties suitable for marine structures. The present invention relates to a method for producing an austenitic / ferritic stainless steel having
【０００２】[0002]
【従来技術】従来より、ＳＵＳ３２９Ｊ１に代表される
オーステナイト・フェライト系ステンレス鋼は、耐蝕
性、特に、海水に対する耐蝕性は、オーステナイト系ス
テンレス鋼のＳＵＳ３０４、ＳＵＳ３１６よりも優れて
おり、海水ポンプ等の海洋構造物に使用されてきてい
る。2. Description of the Related Art Conventionally, austenitic / ferritic stainless steels typified by SUS329J1 have superior corrosion resistance, particularly corrosion resistance to seawater, to austenitic stainless steels such as SUS304 and SUS316, and are suitable for marine pumps such as seawater pumps. It has been used in structures.
【０００３】このような合金は２相温度域において熱処
理を行い、オーステナイト・フェライトの２相混合組織
として、引張強度が約５８８ＭＰａ、伸びが約１８％の
機械的性質を保有させている。Such an alloy is subjected to heat treatment in a two-phase temperature range, and has a mechanical property of a tensile strength of about 588 MPa and an elongation of about 18% as a two-phase mixed structure of austenite and ferrite.
【０００４】また、特殊な加工熱処理を行い、２相微細
粒組織（ｍｉｃｒｏｄｕｐｌｅｘ）とし、適切な温度、
歪速度を与えると数百％もの伸びを示す高速超塑性が発
現することも知られている。この高速超塑性現象は結晶
粒を微細にすることにより歪速度を高速にすることが可
能となる。Further, a special processing heat treatment is performed to form a two-phase fine grain structure (microduplex) at an appropriate temperature,
It is also known that when a strain rate is applied, high-speed superplasticity that exhibits elongation of several hundred percent is exhibited. This high-speed superplasticity phenomenon makes it possible to increase the strain rate by making the crystal grains fine.
【０００５】そして、「日本金属学会誌，１９９０，第
５４巻８号，８８１頁」には、結晶粒径を１μｍ程度に
まで微細にして、歪速度１０-1／ｓのオーダーで、９３
０％の伸びを示したという報告が記載されている。さら
に、歪速度を上昇させて高速超塑性を発現させるために
は、結晶粒をさらに微細にすると有効であることはよく
知られている。[0005] In "Journal of the Japan Institute of Metals, 1990, Vol. 54, No. 8, p. 881", the grain size is made as fine as about 1 .mu.m and the strain rate is 10 -1 / s.
There is a report that it showed 0% elongation. Further, it is well known that it is effective to make the crystal grains finer in order to increase the strain rate and express high-speed superplasticity.
【０００６】この２相微細粒組織（ｍｉｃｒｏｄｕｐｌ
ｅｘ）を得るために、フェライト単相の高温域から急冷
を行って過飽和固溶体とし、次いで、強加工を行い、再
び２相域に昇温してオーステナイトを微細に析出させて
いる。This two-phase fine grain structure (microdupl)
In order to obtain ex), the ferrite single phase is rapidly cooled from a high temperature region to obtain a supersaturated solid solution, then subjected to strong working, and then heated again to the two phase region to finely precipitate austenite.
【０００７】これは加工を行うことによって、オーステ
ナイトの析出サイトの増加を図ることを目的としてい
る。そして、昇温する温度が同じであるならば、強加工
を行う程オーステナイトの析出サイトが増加して、微細
にオーステナイトが分散した組織となる。This is intended to increase the number of austenite precipitation sites by carrying out processing. Then, if the temperature for raising the temperature is the same, the precipitation site of austenite increases as the strength is increased, resulting in a finely dispersed austenite structure.
【０００８】また、結晶粒径が微細になればなる程、強
度、延性のバランスを保持したまま、機械的な特性を向
上させることができることも良く知られていることであ
る。しかし、この方法においては、最終形状の制約か
ら、例えば、圧延では最終形状より決定される板厚によ
り加工度が制約されるため、いくら加工を行っても良好
であるということにはならず、加工度を上昇させるには
自ずから限界があり、結晶粒を微細にすることは困難に
なっている。It is also well known that the finer the crystal grain size, the more the mechanical properties can be improved while maintaining the balance between strength and ductility. However, in this method, due to the restriction of the final shape, for example, in rolling, the workability is restricted by the plate thickness determined from the final shape, so it does not mean that no matter how much processing is performed, There is naturally a limit to increasing the workability, and it is difficult to make crystal grains fine.
【０００９】[0009]
【発明が解決しようとする課題】本発明は上記に説明し
た従来におけるオーステナイト・フェライト系ステンレ
ス鋼の製造方法における種々の問題点を解決したもので
あり、本発明者が鋭意研究を行い、検討を重ねた結果、
従来よりも微細な結晶粒組織を付与することにより機械
的性質を向上させることができる超微細粒組織を有する
オーステナイト・フェライト系ステンレス鋼の製造方法
を開発したのである。DISCLOSURE OF THE INVENTION The present invention has solved various problems in the conventional method for producing austenitic ferritic stainless steel described above, and the present inventor has conducted earnest research and studied. As a result of overlapping
We have developed a method for producing austenite-ferritic stainless steel having an ultrafine grain structure that can improve mechanical properties by imparting a finer grain structure than before.
【００１０】[0010]
【課題を解決するための手段】本発明にかかる超微細粒
組織を有するオーステナイト・フェライト系ステンレス
鋼の製造方法は、オーステナイト・フェライト２相、或
いは、過飽和固溶体であるフェライト単相のオーステナ
イト・フェライト系ステンレス鋼粉末に、機械的合金化
法により強加工を行い、さらに、２相温度域において粉
末の固化を行うことを特徴とする超微細粒組織を有する
オーステナイト・フェライト系ステンレス鋼の製造方法
を第１の発明とし、オーステナイト・フェライト２相、
或いは、過飽和固溶体であるフェライト単相のオーステ
ナイト・フェライト系ステンレス鋼粉末は、４０〜１０
０μｍの径を有することを特徴とする請求項１記載の超
微細粒組織を有するオーステナイト・フェライト系ステ
ンレス鋼の製造方法を第２の発明とし、粉末の固化処理
における加熱温度は、１０００〜１０２０℃であること
を特徴とする請求項１記載の超微細粒組織を有するオー
ステナイト・フェライト系ステンレス鋼の製造方法を第
３の発明とする３つの発明よりなるものである。A method for producing an austenite-ferrite stainless steel having an ultrafine grain structure according to the present invention is austenite-ferrite two-phase or a ferrite single-phase austenite-ferrite system which is a supersaturated solid solution. A method for producing an austenite-ferritic stainless steel having an ultrafine grain structure is characterized in that stainless steel powder is subjected to strong working by a mechanical alloying method, and then the powder is solidified in a two-phase temperature range. 1 invention, austenite ferrite 2 phase,
Alternatively, the ferrite single-phase austenite-ferritic stainless steel powder, which is a supersaturated solid solution, is 40 to 10
The method for producing an austenitic ferritic stainless steel having an ultrafine grain structure according to claim 1 has a diameter of 0 μm as a second invention, and the heating temperature in the solidification treatment of the powder is 1000 to 1020 ° C. According to the third aspect of the present invention, there is provided a method for producing an austenite-ferritic stainless steel having an ultrafine grain structure according to claim 1.
【００１１】本発明にかかる超微細粒組織を有するオー
ステナイト・フェライト系ステンレス鋼の製造方法につ
いて、以下詳細に説明する。The method for producing the austenitic ferritic stainless steel having an ultrafine grain structure according to the present invention will be described in detail below.
【００１２】即ち、超微細粒組織を有するオーステナイ
ト・フェライト系ステンレス鋼の製造方法は、具体的に
は、アトナイズ急冷法により、室温において準安定であ
る過飽和固溶体であるフェライト単相、或いは、平衡状
態であるオーステナイト・フェライト２層を有する粉
末、例えば、粉末粒径４０〜１００μｍのオーステナイ
ト・フェライト系ステンレス鋼粉末を準備して、撹拌
型、遊星型、振動型ボールミル等の高エネルギー型ボー
ルミルによって、２４〜４８時間の機械的合金化処理
（メカニカルグライディング）を行い、最後に熱間静水
圧プレス、或いは、ホットプレス、熱間押出し等の粉末
固化処理を１０００〜１２００℃の温度域において行う
のである。That is, a method for producing an austenitic ferritic stainless steel having an ultrafine grain structure is specifically, by an atomizing quenching method, a ferrite single phase which is a supersaturated solid solution metastable at room temperature, or an equilibrium state. A powder having two layers of austenite / ferrite, for example, austenite / ferrite-based stainless steel powder having a powder particle size of 40 to 100 μm, is prepared by a high energy type ball mill such as a stirring type, planetary type or vibration type ball mill. Mechanical alloying treatment (mechanical gliding) is performed for up to 48 hours, and finally powder solidification treatment such as hot isostatic pressing, hot pressing and hot extrusion is performed in the temperature range of 1000 to 1200 ° C.
【００１３】本発明にかかる超微細粒組織を有するオー
ステナイト・フェライト系ステンレス鋼の製造方法にお
ける機械的合金化法とは、１種または２種以上の金属粉
末に強加工を行い、その加工エネルギーにより室温付近
において金属合金化を行ったり、アモルファス等の準安
定な相に変えることができる方法である。The mechanical alloying method in the method for producing an austenitic ferritic stainless steel having an ultrafine grain structure according to the present invention means one or two or more kinds of metal powders which are subjected to strong working and are subjected to working energy. This is a method in which metal alloying can be performed near room temperature, or a metastable phase such as amorphous can be converted.
【００１４】この方法を準安定なフェライト単相のオー
ステナイト・フェライト系ステンレス鋼粉末に適用する
ことにより、板の圧延等の板厚の制約等最終形状に拘束
されることなく、強加工を行うことができる。By applying this method to a metastable ferritic single-phase austenite-ferritic stainless steel powder, it is possible to perform strong working without being restricted by the final shape such as restriction of plate thickness such as rolling of the plate. You can
【００１５】次いで、その後の固化処理における加熱に
よって、従来の加工熱処理方法では得られないような微
細なオーステナイトを析出させて、特に、強度等の機械
的特性を向上させることができる（加工硬化と微細化を
図ることができる。）。Then, by heating in the subsequent solidification treatment, fine austenite, which cannot be obtained by the conventional thermomechanical treatment method, is precipitated, and in particular, mechanical properties such as strength can be improved (work hardening and It can be miniaturized.)
【００１６】このような機械的合金化法に使用すること
ができる粉末は、４０〜１００μｍの粉末径である準安
定な過飽和固溶体であるフェライト単相、或いは、平衡
状態のオーステナイト・フェライト２層のものが使用す
ることができる。The powder which can be used in such a mechanical alloying method is a ferrite single phase which is a metastable supersaturated solid solution having a powder diameter of 40 to 100 μm, or an austenite-ferrite bilayer in an equilibrium state. Things can be used.
【００１７】この粉末は機械的合金化処理において、加
工、粉砕、圧着を繰り返すことによって、強加工が行わ
れるものであるが、粉末の径が大きすぎると粉末中央部
まで加工が行われず、固化処理時の加熱により粗大なオ
ーステナイトが析出してしまい、機械的特性に悪影響を
及ぼす。In the mechanical alloying treatment, this powder undergoes strong working by repeating working, crushing and pressure bonding. However, if the diameter of the powder is too large, the central part of the powder is not worked and solidifies. Coarse austenite precipitates due to heating during processing, which adversely affects the mechanical properties.
【００１８】従って、微細な粉末を使用すれば粉末サイ
ズ内でオーステナイトの析出が生じるので、良好な結果
が得られるが、粉末の径が４０μｍ未満では機械的合金
化処理時に加工が行えなくなり、また、粉末の径が１０
０μｍを越えると粉末中央部にまで加工が行えない。よ
って、使用する粉末の粉末径は４０〜１００μｍとす
る。Therefore, if a fine powder is used, austenite precipitates within the powder size, and good results are obtained. However, if the diameter of the powder is less than 40 μm, processing cannot be performed during mechanical alloying treatment, and , Powder diameter is 10
If it exceeds 0 μm, it cannot be processed even in the central part of the powder. Therefore, the powder diameter of the powder used is 40 to 100 μm.
【００１９】また、オーステナイトの析出を最大限に利
用するために、使用する粉末はオーステナイトが析出し
ていない準安定な過飽和に固溶しているフェライト単相
の粉末を使用することが望ましい。Further, in order to utilize the precipitation of austenite to the maximum extent, it is desirable that the powder to be used is a ferrite single-phase powder which is solid-dissolved in metastable supersaturation in which austenite is not precipitated.
【００２０】しかし、機械的合金化処理を行うことによ
り、粉末をエネルギーの高い状態にすることが可能であ
り、従って、平衡状態のオーステナイト・フェライト２
層状態の粉末を使用しても、機械的合金化処理中に準安
定状態の過飽和固溶体状態のフェライト単相に遷移する
ので問題はないのである。However, it is possible to bring the powder into a high energy state by carrying out a mechanical alloying treatment, and therefore, the austenite-ferrite 2 in the equilibrium state is used.
Even if the powder in the layer state is used, there is no problem because it transitions to the ferrite single phase in the supersaturated solid solution state in the metastable state during the mechanical alloying process.
【００２１】高エネルギー型ボールミルにより機械的合
金化処理を行う時、処理時間は少なくとも２４時間は必
要であり、処理時間が短い方が生産性からみて効率的で
あるが、２４時間以上の処理を行わないと従来の加工熱
処理法により得られるものの性質を越えることができな
い。When carrying out mechanical alloying treatment with a high energy type ball mill, a treatment time of at least 24 hours is required, and a shorter treatment time is more efficient in terms of productivity, but treatment of 24 hours or more is required. If not done, the properties of those obtained by conventional thermomechanical processing cannot be exceeded.
【００２２】また、機械的合金化処理を２４時間以上行
うことにより粉末がさらに粉砕されて微細になる。そし
て、４８時間を越える時間の処理は機械的合金化処理の
エネルギーを有効に粉末に与えることができないので、
機械的合金化処理時間は２４〜４８時間とする必要があ
る。Further, the mechanical alloying treatment is performed for 24 hours or more, so that the powder is further pulverized and becomes fine. Since the treatment for more than 48 hours cannot effectively impart the energy of the mechanical alloying treatment to the powder,
The mechanical alloying treatment time needs to be 24 to 48 hours.
【００２３】次に、粉末の固化処理方法は、熱間静水圧
プレス（ＨＩＰ）、ホットプレス、熱間押出等により行
うことができるが、加熱温度は合金粉末のオーステナイ
ト・フェライト２相共存域温度の直上である１０００℃
から１０２０℃の範囲の温度とするのがよく、あまり高
温度にまで加熱すると析出オーステナイトの成長速度が
核生成速度を上回り、粗大なオーステナイトを有する組
織となり、機械的性質に問題が発生する。よって、粉末
の固化処理方法における加熱温度は１０００〜１０２０
℃とする。Next, the powder can be solidified by hot isostatic pressing (HIP), hot pressing, hot extrusion, etc., but the heating temperature is the austenite / ferrite two-phase coexisting region temperature of the alloy powder. 1000 ° C just above
It is preferable to set the temperature in the range from 1 to 1020 ° C., and if heated to an excessively high temperature, the growth rate of precipitated austenite exceeds the nucleation rate, resulting in a structure having coarse austenite, which causes a problem in mechanical properties. Therefore, the heating temperature in the powder solidification method is 1000 to 1020.
℃.
【００２４】また、粉末の固化したまま製品形状とする
ことも可能であるが、その後のプレス等の製品形状への
成形を行って、より精密な形状とすることができ、高速
超塑性（成形のし易さ）が生じてくる。It is also possible to make the product shape as it is while the powder is solidified, but it is possible to make a more precise shape by subsequent forming into a product shape such as pressing, and to obtain high-speed superplasticity (forming (Easy to handle) will occur.
【００２５】[0025]
【実 施 例】本発明にかかる超微細粒組織を有するオ
ーステナイト・フェライト系ステンレス鋼の製造方法の
実施例を説明する。[Example] An example of a method for producing an austenite-ferritic stainless steel having an ultrafine grain structure according to the present invention will be described.
【００２６】[0026]
使用粉末 ：Ｃ ０.０３ｗｔ％、Ｓｉ ０.８９ｗｔ
％、Ｍｎ ０.０８２ｗｔ％、Ｐ ０.０２ｗｔ％、Ｓ
０.００７ｗｔ％、Ｎｉ ４.６ｗｔ％、Ｃｒ ２４.８
ｗｔ％、Ｍｏ ２ｗｔ％、Ｏ ０.５ｗｔ％、残部 Ｆ
ｅのＳＵＳ３２９Ｊ１水アトマイズ粉末 粉末径 ： ４４〜１００μｍ 組織 ： 準安定過飽和固溶体のフェライト単相（Ｘ線
回折，組織観察）Powder used: C 0.03 wt%, Si 0.89 wt
%, Mn 0.082 wt%, P 0.02 wt%, S
0.007 wt%, Ni 4.6 wt%, Cr 24.8
wt%, Mo 2 wt%, O 0.5 wt%, balance F
e SUS329J1 water atomized powder Powder diameter: 44-100 μm Structure: Ferrite single phase of metastable supersaturated solid solution (X-ray diffraction, structure observation)
【００２７】機械的合金化処理 ： 遊星型ボールミル（高エネルギー型ボールミルの１種） ボール：粉末の重量比＝５.３：１ 雰囲気：Ａｒガス 回転数１８０ｒｐｍ，２４時間Mechanical alloying treatment: Planetary ball mill (one type of high energy type ball mill) Ball: powder weight ratio = 5.3: 1 Atmosphere: Ar gas Rotation speed 180 rpm, 24 hours
【００２８】得られた粉末を軟鋼カプセルに充填し、１
０００℃の温度に２時間加熱した後、１０００ａｔｍの
条件によりＨＩＰ法により固化を行い、結晶粒、硬さの
測定、また、室温における引張試験を行った。The obtained powder was filled in a mild steel capsule, and 1
After heating at a temperature of 000 ° C. for 2 hours, solidification was carried out by the HIP method under the conditions of 1000 atm, crystal grains and hardness were measured, and a tensile test at room temperature was carried out.
【００２９】１μｍ以下である結晶粒径を有する２相微
細粒組織（ｍｉｃｒｏｄｕｐｌｅｘ）が得られた。引張
強度は６００ＭＰａであった。A two-phase microduplex having a grain size of less than 1 μm was obtained. The tensile strength was 600 MPa.
【００３０】[0030]
【発明の効果】以上説明したように、本発明に係る超微
細粒組織を有するオーステナイト・フェライト系ステン
レス鋼の製造方法は上記の構成であるから、極めて微細
な結晶粒径である超微細粒のオーステナイト・フェライ
トの２相組織を有しており、機械的特性を向上させるこ
とができるという優れた効果を奏するものである。As described above, since the method for producing an austenite-ferritic stainless steel having an ultrafine grain structure according to the present invention has the above constitution, it is possible to obtain an ultrafine grain having an extremely fine grain size. It has a two-phase structure of austenite / ferrite and has an excellent effect that mechanical properties can be improved.
Claims (3)
は、過飽和固溶体であるフェライト単相のオーステナイ
ト・フェライト系ステンレス鋼粉末に、機械的合金化法
により強加工を行い、さらに、２相温度域において粉末
の固化を行うことを特徴とする超微細粒組織を有するオ
ーステナイト・フェライト系ステンレス鋼の製造方法。1. Austenite-ferrite two-phase or a ferrite single-phase austenite-ferrite stainless steel powder which is a supersaturated solid solution is subjected to strong working by a mechanical alloying method, and further, in the two-phase temperature range, A method for producing an austenitic-ferritic stainless steel having an ultrafine grain structure characterized by solidifying.
は、過飽和固溶体であるフェライト単相のオーステナイ
ト・フェライト系ステンレス鋼粉末は、４０〜１００μ
ｍの径を有することを特徴とする請求項１記載の超微細
粒組織を有するオーステナイト・フェライト系ステンレ
ス鋼の製造方法。2. Austenite / ferrite stainless steel powder of austenite / ferrite 2 phase or ferrite single phase which is a supersaturated solid solution is 40 to 100 μm.
The method for producing an austenitic ferritic stainless steel having an ultrafine grain structure according to claim 1, wherein the method has a diameter of m.
００〜１０２０℃であることを特徴とする請求項１記載
の超微細粒組織を有するオーステナイト・フェライト系
ステンレス鋼の製造方法。3. The heating temperature in the solidification treatment of the powder is 10.
The method for producing an austenitic ferritic stainless steel having an ultrafine grain structure according to claim 1, wherein the temperature is from 00 to 1020 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5151213A JPH06336636A (en) | 1993-05-28 | 1993-05-28 | Production of austenitic-ferritic stainless steel having ultrafine-grained structure |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP5151213A JPH06336636A (en) | 1993-05-28 | 1993-05-28 | Production of austenitic-ferritic stainless steel having ultrafine-grained structure |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH06336636A true JPH06336636A (en) | 1994-12-06 |
Family
ID=15513714
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP5151213A Pending JPH06336636A (en) | 1993-05-28 | 1993-05-28 | Production of austenitic-ferritic stainless steel having ultrafine-grained structure |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH06336636A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2017504723A (en) * | 2013-12-27 | 2017-02-09 | サンドビック インテレクチュアル プロパティー アクティエボラーグ | Corrosion-resistant duplex steel alloys, articles made from corrosion-resistant duplex steel alloys, and methods of making such alloys |
| KR20180123499A (en) * | 2016-03-15 | 2018-11-16 | 케이에스비 에스이 앤드 코. 카게아아 | A method for producing a component from a duplex steel and a method for producing the component |
-
1993
- 1993-05-28 JP JP5151213A patent/JPH06336636A/en active Pending
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2017504723A (en) * | 2013-12-27 | 2017-02-09 | サンドビック インテレクチュアル プロパティー アクティエボラーグ | Corrosion-resistant duplex steel alloys, articles made from corrosion-resistant duplex steel alloys, and methods of making such alloys |
| JP2019151928A (en) * | 2013-12-27 | 2019-09-12 | サンドビック インテレクチュアル プロパティー アクティエボラーグ | Corrosion resistant duplex steel alloy, objects made of corrosion resistant duplex steel alloy, and method of making such alloy |
| KR20180123499A (en) * | 2016-03-15 | 2018-11-16 | 케이에스비 에스이 앤드 코. 카게아아 | A method for producing a component from a duplex steel and a method for producing the component |
| CN109070215A (en) * | 2016-03-15 | 2018-12-21 | Ksb 股份公司 | The method of component is manufactured by dual phase steel and passes through the component that this method manufactures |
| JP2019516009A (en) * | 2016-03-15 | 2019-06-13 | カーエスベー ソシエタス ヨーロピア ウント コンパニー コマンディート ゲゼルシャフト アウフ アクチェンＫＳＢ ＳＥ ＆ Ｃｏ． ＫＧａＡ | Method for producing parts from duplex stainless steel, and parts produced using said method |
| CN109070215B (en) * | 2016-03-15 | 2021-07-02 | Ksb股份有限公司 | Method for producing a component from a dual-phase steel and component produced by said method |
| US11059102B2 (en) | 2016-03-15 | 2021-07-13 | KSB SE & Co. KGaA | Method for producing components from a duplex steel, and components produced using said method |
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