JPS62222044A - Hot-working method for two-phase stainless steel powder - Google Patents
Hot-working method for two-phase stainless steel powderInfo
- Publication number
- JPS62222044A JPS62222044A JP6547786A JP6547786A JPS62222044A JP S62222044 A JPS62222044 A JP S62222044A JP 6547786 A JP6547786 A JP 6547786A JP 6547786 A JP6547786 A JP 6547786A JP S62222044 A JPS62222044 A JP S62222044A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- less
- phase
- duplex stainless
- steel
- 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
- 239000000843 powder Substances 0.000 title claims abstract description 37
- 238000000034 method Methods 0.000 title claims description 20
- 229910001220 stainless steel Inorganic materials 0.000 title abstract description 21
- 239000010935 stainless steel Substances 0.000 title abstract description 17
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 35
- 239000010959 steel Substances 0.000 claims abstract description 35
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 18
- 239000000203 mixture Substances 0.000 claims abstract description 12
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 229910052742 iron Inorganic materials 0.000 claims abstract description 10
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 10
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 9
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 5
- 229910052802 copper Inorganic materials 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 4
- 229910001039 duplex stainless steel Inorganic materials 0.000 claims description 33
- 229910000859 α-Fe Inorganic materials 0.000 claims description 11
- 229910001566 austenite Inorganic materials 0.000 claims description 8
- 238000003672 processing method Methods 0.000 claims description 2
- 230000001747 exhibiting effect Effects 0.000 claims 1
- 238000001513 hot isostatic pressing Methods 0.000 abstract description 2
- 229910052717 sulfur Inorganic materials 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 28
- 238000012545 processing Methods 0.000 description 21
- 238000005260 corrosion Methods 0.000 description 16
- 239000011651 chromium Substances 0.000 description 15
- 230000007797 corrosion Effects 0.000 description 15
- 238000004519 manufacturing process Methods 0.000 description 8
- 230000000694 effects Effects 0.000 description 7
- 238000005242 forging Methods 0.000 description 7
- 239000010949 copper Substances 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 238000001125 extrusion Methods 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- 239000001301 oxygen Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 238000007711 solidification Methods 0.000 description 4
- 230000008023 solidification Effects 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 238000000889 atomisation Methods 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 239000002775 capsule Substances 0.000 description 3
- 238000007796 conventional method Methods 0.000 description 3
- 238000006073 displacement reaction Methods 0.000 description 3
- 238000009689 gas atomisation Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 238000001192 hot extrusion Methods 0.000 description 2
- 238000003754 machining Methods 0.000 description 2
- 230000008569 process Effects 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- 101150018425 Cr1l gene Proteins 0.000 description 1
- 229910000881 Cu alloy Inorganic materials 0.000 description 1
- 238000001994 activation Methods 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000005587 bubbling Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 238000012733 comparative method Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000012768 molten material Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 238000005191 phase separation Methods 0.000 description 1
- 229910052761 rare earth metal Inorganic materials 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、常温付近でフェライト相とオーステナイト相
の二相組織を呈する、Ｆｅ、 ＣｒおよびＮｉを主成分
とし、必要に応じてＭｏｌＮを含有する二相ステンレス
鋼系アトマイズ鋼粉を熱間で超塑性加工する方法に関す
る。Detailed Description of the Invention (Industrial Field of Application) The present invention is directed to a material containing Fe, Cr, and Ni as main components, which exhibits a two-phase structure of ferrite phase and austenite phase near room temperature, and optionally contains MolN. This invention relates to a method for hot superplastic working of duplex stainless steel atomized steel powder.
（従来の技術）
一般に、二相ステンレス鋼は塩化物環境下で優れた耐応
力腐食割れ性とオーステナイトステンレス鋼並みの良好
な溶接性とを有する高強度高耐食性ステンレス鋼として
知られており、各種の分野で幅広く使用されるようにな
ってきている。しかしながら、一方でσ脆化等による難
加工材としても知られている。(Prior art) Duplex stainless steel is generally known as a high-strength, high-corrosion-resistant stainless steel that has excellent stress corrosion cracking resistance in a chloride environment and good weldability comparable to austenitic stainless steel. It is becoming widely used in the field of However, it is also known as a material that is difficult to machine due to σ embrittlement.
ところで、ステンレス鋼には、マルテンサイト系、フェ
ライト系、二相系、オーステナイト系のステンレス鋼が
あり、このうち、フェライト系ステンレス鋼は安価で優
れた耐応力腐食割れ性を有するという特徴があるが、靭
性、溶接性に劣ることが欠点である。オーステナイト系
ステンレス鋼は、優れた靭性と耐食性を有しているが、
耐応力腐食割れ性（以下、「耐ＳＣＣ性」という）に劣
るという欠点がある。By the way, there are three types of stainless steel: martensitic, ferritic, duplex, and austenitic. Among these, ferritic stainless steel is characterized by being inexpensive and having excellent stress corrosion cracking resistance. The disadvantages are poor toughness and weldability. Austenitic stainless steel has excellent toughness and corrosion resistance, but
It has a drawback of being inferior in stress corrosion cracking resistance (hereinafter referred to as "SCC resistance").
二相系ステンレス鋼はこれら両者の長所を兼ね備えた優
れた特徴を有しており、高強度であることもあって、近
年その利用分野を拡大している。Duplex stainless steel has excellent features that combine the advantages of both of these, and due to its high strength, its fields of use have been expanding in recent years.
現在、１ＢＣｒ系の二相ステンレス鋼、２２Ｃｒ系の二
相ステンレス鋼、２５Ｃｒ系の二相ステンレス鋼などが
市販されているが、最も大きな製造上の問題点の一つに
熱間加工性の悪さがある。最近では、熱間加工性に有害
なＳや酸素を低減するなどの対策により、仮や管のよう
に形状の単純なものや、比較的簡単な形状の鍛造品の製
造は可能となってきたが、複雑な形状の部品、たとえば
管継手やバルブなどの製造は極めて困難であり、未だに
歩留まりや能率の悪い機械加工に錬らざるを得ないのが
現状である。Currently, 1BCr duplex stainless steel, 22Cr duplex stainless steel, 25Cr duplex stainless steel, etc. are commercially available, but one of the biggest manufacturing problems is poor hot workability. There is. Recently, through measures such as reducing S and oxygen, which are harmful to hot workability, it has become possible to manufacture forged products with simple shapes such as temporary pipes and relatively simple shapes. However, manufacturing parts with complex shapes, such as pipe joints and valves, is extremely difficult, and the current situation is that we still have to resort to machining, which has low yields and low efficiency.
ところで、粉末法によるステンレス鋼の製造は、ガスア
トマイズ法の発展とともに近年注目を浴びている。鋼中
酸素量の低い良質のステンレス鋼粉の大量生産方式の確
立は新しい用途開発を促している。たとえば、１９８４
年ＡＳＭ Ｉｎｔｅｒｎａｔｉｏｎａｌ Ｃｏｎｆｅｒ
ｅｎｃｅ ｏｎ Ｎｅｗ Ｄｅｖｅｌｏｐ＋ｍｅｎｔｓ
においてＣ１ｅａｓ Ｔ。Incidentally, the production of stainless steel by the powder method has been attracting attention in recent years along with the development of the gas atomization method. The establishment of a mass production method for high-quality stainless steel powder with low oxygen content in the steel is encouraging the development of new applications. For example, 1984
ASM International Conference
ence on New Develop + ments
In C1eas T.
ｒｎｂｅｒｇが報告した８４１０−０１３報告にみるよ
うに、ガスアトマイズ法により製造したステンレス鋼粉
を炭素鋼製カプセルに充填し、冷間静水圧法によりカプ
セルを高密度化してビレットとし、熱間押出し法により
継目無し管とすることが行われている。As seen in the 8410-013 report reported by RNBERG, stainless steel powder produced by gas atomization is filled into a carbon steel capsule, the capsule is densified into a billet by cold isostatic pressure, and the capsule is made into a billet by hot extrusion. Seamless pipes are being used.
この方法はＴＰ ３２９などの二相ステンレス鋼にも適
用されている。しかし、その場合σ相の生成域での加工
を避けるために比較的高温に加熱した後加工が開始され
るため、押出し初期にはフェライト単相域での加工が行
われている。また、熱間押出し製管であり、押出し速度
のコントロールも行われていないことより、歪速度ば１
ｘｌＯ” １／ｓｅｃを超えたものとなっている。This method has also been applied to duplex stainless steels such as TP 329. However, in this case, processing is started after heating to a relatively high temperature in order to avoid processing in the σ phase generation region, so processing is performed in the ferrite single phase region at the initial stage of extrusion. In addition, since the pipe is made by hot extrusion and the extrusion speed is not controlled, the strain rate is 1.
xlO” 1/sec.
ステンレス鋼粉を原料として焼結あるいは圧粉成形、接
合して密度を高め、従来の造塊材と同等の機能と性質を
もたせた場合の特徴は、（１１溶解材にみられる造塊時
の凝固偏析に起因する成分変動がステンレス鋼粉を原料
とした鋼材には認められないこと、（２）鋼中のＳ％Ｐ
の偏析が小さく、非金属介在物も細かく分散しているこ
と、（３）高温での加工性が悪く、製造が困難であった
ものが、比較的容易に製造可能となること、＋４１ Ｖ
ＩＡ粉を含む複合材料が製造可能であること、などであ
る。When stainless steel powder is used as a raw material, it is sintered, compacted, and bonded to increase its density and have the same functions and properties as conventional agglomerates. Component fluctuations caused by solidification segregation are not observed in steel materials made from stainless steel powder; (2) S%P in steel;
(3) What used to be difficult to manufacture due to poor workability at high temperatures can now be manufactured relatively easily. +41 V
For example, it is possible to manufacture composite materials containing IA powder.
他方、超塑性加工に関する従来技術としては、既に多く
の特許が出願されており、本件特許出願人も、たとえば
、特願昭６０−６４１６３号および同６０−８４０８７
号として提案している。On the other hand, many patents have already been filed regarding conventional techniques related to superplastic working, and the applicant of this patent has also filed patent applications, such as Japanese Patent Application No. 60-64163 and No. 60-84087.
It is proposed as a number.
また、一般の文献としては、「鉄と鋼Ｊ 、 ７０ （
。In addition, as a general literature, “Tetsu to Hagane J, 70 (
.
１９８４） ｐ、 ２１６８がある。1984) p. 2168.
これら従来のものはいずれも溶解材を熱間圧延するもの
である。粉末に関するものとしては、特公昭５５−１０
６４２号があるが、これは温度サイクルを与える、Ｆｅ
粉末の変態超塑性を利用するものである。All of these conventional methods hot-roll molten material. As for powder, the special publication 1986-10
There is No. 642, which gives a temperature cycle, Fe
This utilizes the transformation superplasticity of powder.
このように、従来のいずれの文献においても、二相系ス
テンレス鋼のアトマイズ鋼粉を超塑性加工に利用したと
の記述はなく、またそのときの優れた超塑性加工性を示
すものはない。As described above, none of the conventional literature describes the use of atomized steel powder of duplex stainless steel for superplastic working, and there is nothing that shows the excellent superplastic workability at that time.
（発明が解決しようとする問題点）
ステンレス鋼の使用環境は年々厳しくなるとともに、他
方では使用者側によりコストの低減要求が常に要請され
ている。二相系ステンレス鋼においても、安価な高耐食
、高強度鋼として、また優れた耐ＳＣＣ性を存するステ
ンレス鋼としての用途は漸次拡大している。(Problems to be Solved by the Invention) The environment in which stainless steel is used is becoming more severe year by year, and on the other hand, there are constant demands from users to reduce costs. The use of duplex stainless steel as an inexpensive, highly corrosion-resistant, high-strength steel, and as a stainless steel with excellent SCC resistance is gradually expanding.
しかしながら、二相系ステンレス鋼においては、周知の
ように、熱間での製品加工時の耳割れに代表される加工
性の悪さ、およびσ脆化による靭性劣化の問題は極めて
重要であり、さらにまた、薄板とした場合には、圧延り
方向、Ｔ方向での引張性質の違い、いわゆる異方性の大
なることは、用途拡大の妨げとなっている。また、二相
系ステンレス鋼は冷間での加工性においても決して優れ
た加工性を有しているとはいえない。However, as is well known, in duplex stainless steel, problems such as poor workability typified by edge cracking during hot processing and toughness deterioration due to σ embrittlement are extremely important. In addition, in the case of a thin plate, the difference in tensile properties in the rolling direction and the T direction, that is, the large anisotropy, hinders the expansion of applications. Furthermore, duplex stainless steel cannot be said to have excellent cold workability.
（発明の目的）
本発明はこうした問題を一挙に解決しようとするもので
あり、その第一の目的は、二相系ステンレスアトマイズ
鋼粉を原料とし、その焼結体（粉末が拡散接合した状態
を意味する）も含め任意の形状に容易に加工しうる熱間
加工方法を提供することにある。(Purpose of the Invention) The present invention attempts to solve these problems all at once, and its first purpose is to produce a sintered body (a state in which the powder is diffusion bonded) using two-phase stainless atomized steel powder as a raw material. The object of the present invention is to provide a hot working method that allows easy processing into any shape, including (meaning .).
また別の本発明の目的は、熱間あるいは冷間での加工が
σ相析出により困難である高Ｃｒ、高Ｍ〇二相系ステン
レス鋼を容易に加工しうる熱間加工方法を提供すること
である。Another object of the present invention is to provide a hot working method that can easily work high Cr, high M0 duplex stainless steel, which is difficult to work in hot or cold due to σ phase precipitation. It is.
またさらに別の目的は、歩留良く、成分偏析の少ない二
相系ステンレス鋼を容易に加工しうる熱間加工方法を提
供することにある。Still another object is to provide a hot working method that can easily process duplex stainless steel with good yield and low component segregation.
なおまた別の目的は、二相系ステンレス鋼の異方性の少
ない加工方法を提供することにある。Yet another object is to provide a method for processing duplex stainless steel with less anisotropy.
なおさらに別の目的は、二相系ステンレス鋼の加工方法
において、素材とするための予備加工、予備成形が不要
であるか、または容易である熱間加工方法を提供するこ
とである。Yet another object is to provide a hot working method for duplex stainless steel in which preliminary processing and preforming for preparing a raw material are unnecessary or easy.
（問題点を解決するための手段）
かかる目的を達成すべく、本発明者らが種々検討を重ね
たところ、用いる素材を従来の溶製材よりアトマイズ法
により製造したステンレス鋼粉とすることに着目し、さ
らに検討をつづけ、以下の点を知見し、本発明を完成し
た。(Means for Solving the Problems) In order to achieve this objective, the present inventors conducted various studies and focused on using stainless steel powder produced by the atomization method as the material instead of conventional melted material. However, after further investigation, the following points were discovered and the present invention was completed.
すなわち、アトマイズ鋼粉は、凝固速度が従来の溶製材
に比べ著しく大きいため、凝固時の成分偏析が極めて小
さい、また、α、γ二相への分離も充分には行われず、
分散相の凝集も充分に進行していない。その結果として
、アトマイズ鋼粉より製造した焼結二相ステンレス鋼の
分散相は通常の溶製材に比べ、極めて細かい分散相を有
していス−
このように、超塑性変形にとっては分散相が均一に細く
分散することは極めて望ましい状態であり、かかる２相
ステンレス鋼アトマイズ銅粉は素材として極めて望まし
いものであり、その超塑性効果も溶解材のそれに比較し
て大幅に上回るものである。In other words, since the solidification rate of atomized steel powder is significantly higher than that of conventional ingot material, the segregation of components during solidification is extremely small, and the separation into α and γ two phases is not sufficient.
The aggregation of the dispersed phase also did not progress sufficiently. As a result, the dispersed phase of sintered duplex stainless steel produced from atomized steel powder has an extremely fine dispersed phase compared to that of ordinary ingot material. It is an extremely desirable state that the copper powder is finely dispersed, and such a duplex stainless steel atomized copper powder is extremely desirable as a material, and its superplastic effect is greatly superior to that of the melted material.
その他、アトマイズ鋼粉とした時には、鋼粉表面の酸化
スケールあるいは吸着酸素により加工後の鋼中酸素濃度
が若干高いなどの不利な点はあるにしても、次のような
利点が見られる。In addition, when atomized steel powder is used, although there are disadvantages such as a slightly high oxygen concentration in the steel after processing due to oxidized scale on the surface of the steel powder or adsorbed oxygen, the following advantages can be seen.
■成分偏析が小さい。■Less component segregation.
■良好な超塑性性質により、変形抵抗がより低減し、か
つ成形性が向上する。■Good superplastic properties further reduce deformation resistance and improve formability.
■低温での加工が可能となるため、製品の品質が向上す
る。■Product quality improves as processing at low temperatures becomes possible.
■熱間あるいは冷間での加工がσ相析出で極めて困難で
ある成分系の二相系ステンレス鋼も素材とすることが可
能である。■It is also possible to use duplex stainless steel as a material, which is extremely difficult to work in hot or cold due to precipitation of the sigma phase.
■歩留りが良い。■Good yield.
■素材にするための予備加工、予備成形が不要または容
易である。■Preliminary processing and preforming to make the material is unnecessary or easy.
■Ｎ２ガスアトマイズあるいは液体窒素中でアトマイズ
直後の急冷を行うことにより、溶製材では凝固時のバブ
リング等で困難な高Ｎ化を図ることができる。Ｎは、α
、γ二相分離が進行する温度領域での拡散が速いため、
超塑性変形時におけるα、γ分配を促進する効果があり
、超塑性変形には望ましい。(2) By performing N2 gas atomization or rapid cooling immediately after atomization in liquid nitrogen, it is possible to achieve a high N content, which is difficult to achieve with ingot material due to bubbling during solidification. N is α
, because diffusion is fast in the temperature range where γ two-phase separation progresses,
It has the effect of promoting α and γ distribution during superplastic deformation, and is desirable for superplastic deformation.
■加工時に方向性がない。■There is no direction during processing.
よって、本発明の要旨とするところは、Ｆｅ、 Ｃｒお
よびＮｉを主成分とし、必要に応じてＭｏ、 Ｎを含有
する、常温付近でフェライト相とオーステナイト相の二
相組織を呈する二相ステンレス銅系アトマイズ直後の集
合体を、７００℃以上、〔（フェライト単相となる温度
） −１００℃〕以下の温度域で、Ｉ Ｘ １０−’１
／ｓｅｃ以上、１ ｘｌＯ’ １／ｓｅｃ以下の歪速度
で変形させることを特徴とする、二相ステンレス鋼粉の
熱間加工方法である。Therefore, the gist of the present invention is to produce a two-phase stainless steel copper alloy which exhibits a two-phase structure of a ferrite phase and an austenite phase at around room temperature, which contains Fe, Cr and Ni as main components, and optionally contains Mo and N. The aggregate immediately after system atomization is heated to I
This is a hot working method for duplex stainless steel powder, which is characterized by deforming at a strain rate of 1/sec or more and 1 xlO' 1/sec or less.
本発明の別の態様によれば、上記二相ステンレス鋼系ア
トマイズ鋼粉を、熱間静水圧プレス装置において、上記
温度範囲に加熱し、上記歪速度範囲で変形・緻密化する
ことを特徴とする、二相ステンレス鋼系アトマイズ鋼粉
の熱間静水圧加工方法が提供される。According to another aspect of the present invention, the duplex stainless steel atomized steel powder is heated to the temperature range described above in a hot isostatic press apparatus, and deformed and densified at the strain rate range described above. A method for hot isostatic processing of duplex stainless steel atomized steel powder is provided.
なお、本発明が対象とする鋼種は、まず、一般的には、
Ｆｅ、 ＣｒおよびＮｉを主成分とし、必要に応じてＭ
ｏ、 Ｎを含有する、常温付近でフェライト相とオース
テナイト相の二相組織を呈する二相ステンレス鋼であれ
ば、特に制限はなく、二相共存下で超塑性加工を行い、
超塑性変形を達成するという本発明の目的が達成される
のである。しかし、好ましくは、かかる鋼種は、重量％
で、Ｃｒ： １２．０〜３５．０％、Ｎｉ： ３．０〜
１８．０％、 残部Ｆｅおよび付随不純物から成るｗ４
組成を有するものである。このように高Ｃｒ系鋼は難加
工材として知られているものである。The steel types targeted by the present invention are generally:
The main components are Fe, Cr and Ni, and M as necessary.
There is no particular restriction as long as the stainless steel contains o, N and exhibits a two-phase structure of a ferrite phase and an austenite phase at around room temperature, and superplastic working is performed under the coexistence of two phases.
The objective of the invention to achieve superplastic deformation is thus achieved. However, preferably such steel grades are
So, Cr: 12.0~35.0%, Ni: 3.0~
18.0% w4, balance consisting of Fe and incidental impurities
It has a composition. As described above, high Cr steel is known as a material that is difficult to machine.
さらに好ましくは、前記２相ステンレス鋼は、重量％で
、
Ｃｒ： １２．０〜３５．０％、Ｎｉ： ３．０〜１８
．０％、Ｃ： ０．０５％以下、 Ｓｉ： ０．０５〜
５．０％、Ｍｎ： ０．０５〜８．０％、Ｍｏ： ５．
０％以下、Ｎ ： ｏ、０５〜０．８％、Ｃｕ： ０，
８％以下、Ｐ ： ０．０５％以下、 Ｓ ： ０．０
０５％以下、残部Ｆｅおよび付随不純物
から成るａｍ成を有するものである。More preferably, the duplex stainless steel contains, in weight percent, Cr: 12.0 to 35.0%, Ni: 3.0 to 18%.
．． 0%, C: 0.05% or less, Si: 0.05~
5.0%, Mn: 0.05-8.0%, Mo: 5.
0% or less, N: o, 05-0.8%, Cu: 0,
8% or less, P: 0.05% or less, S: 0.0
It has an am composition of 0.05% or less, the balance consisting of Fe and incidental impurities.
なお、ここに「集合体」とは、圧粉体あるいは焼結体を
いい、その他車なる鋼粉の混合体をも意味する。しかし
、−ｉには焼結体であり、本発明によればそれに鍛造、
押出し、熱間静水圧加工、あるいはそれらを組合せて加
えるのである。Note that the term "aggregate" herein refers to a green compact or a sintered compact, and also refers to a mixture of steel powder, such as a car. However, -i is a sintered body, and according to the present invention, it is forged,
It can be applied by extrusion, hot isostatic pressing, or a combination thereof.
集合体に全体的に均一な成形力がかかる場合にはともか
く、それが不均一なときはその歪速度は超塑性変形が現
に行われている領域での歪み速度をもって、本発明にい
う歪み速度とする。Regardless of when a uniform forming force is applied to the aggregate as a whole, when it is uneven, the strain rate is the strain rate in the area where superplastic deformation is actually taking place, and the strain rate referred to in the present invention is shall be.
（作用）
本発明において、ｗ４組成および加工条件を上述のよう
に限定した理由は次の通りである。なお、本明細書を通
じて、「％」は特に指定のない限り「重量％」である。(Function) In the present invention, the reason why the w4 composition and processing conditions are limited as described above is as follows. Note that throughout this specification, "%" means "% by weight" unless otherwise specified.
Ｃｒ ： Ｃｒは耐食性を左右する基本元素であり、耐
食性確保のため下限を１２．０％に定める。Ｃｒ濃度が
高いほど耐食性は改善されるが、他方で鋼質を脆くする
ので、上限を３５．０％と定めた。Cr: Cr is a basic element that affects corrosion resistance, and the lower limit is set at 12.0% to ensure corrosion resistance. The higher the Cr concentration, the better the corrosion resistance, but on the other hand, it makes the steel brittle, so the upper limit was set at 35.0%.
Ｎｉ ： ＮｉはＣｒ、 Ｍｏとならんで耐食性を左右
する合金元素であり、さらにはＮとならんで有効なオー
ステナイト生成元素である。Ｃｒｔ！ａ度１２．０〜３
５．０％において二相組織とするには、Ｎｉは３．０〜
１８゜０％必要である。Ni: Ni is an alloying element that affects corrosion resistance along with Cr and Mo, and is also an effective austenite forming element along with N. Crt! A degree 12.0-3
To form a two-phase structure at 5.0%, Ni must be 3.0~
18°0% is required.
Ｍｏ ： ＭｏはＣｒ、 Ｎｉとならんで耐食性を左右
する元素であり、耐食性を改善する効果が極めて大きい
。Mo: Along with Cr and Ni, Mo is an element that affects corrosion resistance, and has an extremely large effect on improving corrosion resistance.
Ｍｏは高価な合金元素であり、必要に応じて添加する。Mo is an expensive alloying element and is added as necessary.
ただしσ相の析出を著しく促進するため、上限は５．０
％とする。However, the upper limit is 5.0 because it significantly promotes the precipitation of the σ phase.
%.
ＮＵＮはＮｉ、 Ｃとならんで耐食性を左右する元素で
あり、特に高温でのオーステナイト安定に対し効果を有
する元素である。Ｎは必要に応じて０．０５〜０．８％
の範囲で積極的に添加する。NUN, along with Ni and C, is an element that affects corrosion resistance, and is particularly effective for stabilizing austenite at high temperatures. N is 0.05-0.8% as necessary
Actively add within the range.
本発明鋼においてはこれらの元素の他に、所望により下
記元素を次のように制限ないし添加する。In addition to these elements, in the steel of the present invention, the following elements may be restricted or added as desired.
Ｃ：Ｃはクロム炭化物を生成し、有効Ｃｒ１ｌを減ずる
ため、耐食性を損なう場合がある。望ましくは、０．０
５％以下とする。C: C produces chromium carbide and reduces effective Cr1l, which may impair corrosion resistance. Preferably 0.0
5% or less.
Ｓｉ：Ｓｉは有効な脱酸元素である。また、高温での耐
酸化性を向上させる働きがある。望ましくは０．０５〜
５，０％の範囲内で添加する。Si: Si is an effective deoxidizing element. It also works to improve oxidation resistance at high temperatures. Desirably 0.05~
Add within the range of 5.0%.
Ｍｎ ： Ｍｎは鋼中のＳをＭｎＳとして固定する働き
がある有効な元素である。また、Ｓｉと共存することに
より脱酸効果もある。他方、ＭｎはＮｉ、 Ｎなどとな
らんで有効なオーステナイト生成元素であり、また鋼中
へのＮ溶解度を大きくする働きがある。望ましくは、０
．０５〜８．０％の範囲内で添加する。０．０５％未満
では添加の効果がなり、８゜０％を越えて含有させる場
合には製造性が悪くなるとともに、素材として硬くなり
、脆くなる。Mn: Mn is an effective element that has the function of fixing S in steel as MnS. Further, by coexisting with Si, it also has a deoxidizing effect. On the other hand, Mn is an effective austenite-forming element along with Ni, N, etc., and also has the function of increasing the solubility of N in steel. Preferably 0
．． It is added within the range of 0.05 to 8.0%. If the content is less than 0.05%, the effect of addition is lost, and if the content exceeds 8.0%, manufacturability deteriorates and the material becomes hard and brittle.
Ｐ：Ｐは不純物であり、望ましくは０．０５％以下に制
限する。P: P is an impurity and is desirably limited to 0.05% or less.
ＳＯ３も不純物であり、耐食性を劣化させるとともに熱
間での加工性を劣化させる。Ｓは低ければ低いほど望ま
しい、望ましくはｏ、ｏｏｓ％以下とする。SO3 is also an impurity, which deteriorates corrosion resistance and hot workability. The lower S is, the more desirable it is, and desirably it is less than o, oos%.
Ｃｕ ： Ｃｕは耐食性を改善する働きがある。ただし
、Ｃｕを多量に添加すると鋼質を脆くするので、添加す
る場合には望ましくは０．８％以下とする。Cu: Cu has the function of improving corrosion resistance. However, if a large amount of Cu is added, the steel becomes brittle, so if Cu is added, it is preferably 0.8% or less.
その他の不純物元素として、ｔｏｏ ｐｐｍ以下のＢ、
０．１％未満のＡＩ、少量の希土類元素、Ｃａ、 Ｍｇ
などを含有する場合がある。Other impurity elements include too ppm or less of B,
Less than 0.1% AI, small amounts of rare earth elements, Ca, Mg
It may contain etc.
ここで、より好ましくは、熱間加工を行うｔｏｏ。Here, more preferably hot working is performed.
℃近辺でフェライトとオーステナイトの相比がほぼ等し
くなるように、
Ｃｒ ｅｑ ＝ Ｃｒ ＋ Ｍｏ ＋ １．５ＳｉＮｉ
ｅｑ ＝ Ｎｉ ＋ ０．５Ｍｎ ＋ ３０Ｃ＋ ２
５Ｎで示されるＣｒ ｅｑがＮｉ ｅｑの約３倍となる
ものがよい、このことは、熱間変形を好ましくするのみ
ならず、製品の性質確保の点でも重要である。Cr eq = Cr + Mo + 1.5SiNi so that the phase ratio of ferrite and austenite is almost equal around ℃.
eq = Ni + 0.5Mn + 30C + 2
It is preferable that the Cr eq expressed in 5N is about three times the Ni eq. This is important not only to make hot deformation favorable but also to ensure the properties of the product.
変形塩度域を７００℃以上、〔（フェライト単相となる
温度）−１００℃〕以下としたのは、７００℃未満では
超塑性に必要なσ相の析出やγ相の再結晶などの熱活性
化過程の働きが不充分となって、超塑性が得にくくなる
ためである。他方、上限温度を〔（フェライト単相とな
る温度）−１００℃〕以下としたのは、この温度を超え
るとγ相の量が極端に減って第二相としてのγ相が分散
球状化し、α相の再結晶を促す効果が得られないためで
ある。The reason why we set the deformation salinity range to be above 700℃ and below [(temperature at which ferrite becomes single phase) -100℃] is because below 700℃, heat such as precipitation of σ phase and recrystallization of γ phase, which are necessary for superplasticity, is set. This is because the activation process becomes insufficient, making it difficult to obtain superplasticity. On the other hand, the reason why the upper limit temperature was set to below [(temperature at which ferrite becomes single phase) -100°C] is because when this temperature is exceeded, the amount of γ phase decreases extremely and the γ phase as a second phase becomes dispersed and spheroidized. This is because the effect of promoting recrystallization of the α phase cannot be obtained.
通常α単相となる温度は１２００〜１３５０℃程度であ
り、より好ましい範囲はおよそ８００−１１００℃であ
る。Usually, the temperature at which α single phase is formed is about 1200 to 1350°C, and the more preferable range is about 800 to 1100°C.
本発明においては、型鍛造あるいは押出し成形を行う場
合、適切な型材を必要とするが、そのような１１００℃
以下の加工温度領域においては、ＳＵＳ ３１０等のオ
ーステナイト系ステンレス鋼、さらにはＮｉ基の高合金
なども型材として十分な高温強度を有しており、利用可
能であうで、本発明の実施を容易とする一つの大きな製
造上の長所となっている。In the present invention, when performing die forging or extrusion molding, an appropriate mold material is required, but such 1100 ° C.
In the following processing temperature range, austenitic stainless steels such as SUS 310, and even Ni-based high alloys have sufficient high temperature strength as mold materials and can be used, making it easier to implement the present invention. This is one major manufacturing advantage.
本発明にあって、歪み速度もその構成要件の１つであり
、超塑性現象を発現させるためにはある一定の歪速度が
規定される。本発明において変形時の歪速度（ε）を１
０４〜ｔｏ’ １／ｓｅｅの範囲としたのは、この範囲
を外れると上記の変形中の組織変化が変形中に生じにく
くなって、超塑性が得にくくなるからである。一般に実
用上好ましいのは、１０−’〜１０−’ １／ｓｅｅで
ある。In the present invention, strain rate is also one of its constituent requirements, and a certain strain rate is specified in order to cause the superplastic phenomenon to occur. In the present invention, the strain rate (ε) during deformation is set to 1
The reason for setting the range to be 04 to '1/see is that outside this range, the above-mentioned structural change during deformation becomes difficult to occur during deformation, making it difficult to obtain superplasticity. Generally preferred in practical terms is 10-' to 10-' 1/see.
次に、実施例によって本発明をさらに具体的に説明する
。Next, the present invention will be explained in more detail with reference to Examples.
大隻■上
第１表に示される成分組成の二相ステンレス銅粉をＳＯ
５３１０製金型内に充填して、１０５０℃に加熱し、２
ｋｇｆ／ｗ”の静水圧下に５分間保持した後、急冷し
て焼結体を作成した。雰囲気はＮｔガス雰囲気であり、
露点は一４５℃であった。Two-phase stainless steel copper powder with the composition shown in Table 1 above is SO
5310 mold, heated to 1050℃,
After holding it under a hydrostatic pressure of ``kgf/w'' for 5 minutes, it was rapidly cooled to create a sintered body.The atmosphere was an Nt gas atmosphere.
The dew point was -45°C.
得られた焼結体より丸棒引張試験片を作成し、熱間での
引張変形を施し、伸びを求めた。A round bar tensile test piece was prepared from the obtained sintered body, subjected to hot tensile deformation, and elongation was determined.
得られた結果を第２表にまとめて示す。The results obtained are summarized in Table 2.
比較鋼として示した二相ステンレス鋼１６〜１９は、そ
れぞれ供試したアトマイズ鋼粉と同成分を有する溶解材
であり、通常の鍛造・熱延材である。Duplex stainless steels 16 to 19 shown as comparative steels are melted materials having the same composition as the atomized steel powder used, and are ordinary forged and hot rolled materials.
第２表に示された結果からも、本発明方法によれば各二
相ステンレス鋼アトマイズ鋼粉焼結体はいずれも高い歪
速度の変形であるにもかかわらず、すべて２００％以上
の極めて良好な伸びを示しており、この条件での大変形
が容易に可能であることが明らかである。The results shown in Table 2 also show that according to the method of the present invention, the duplex stainless steel atomized steel powder sintered bodies were all deformed at a high strain rate, but were all extremely good, exceeding 200%. It is clear that large deformations are easily possible under these conditions.
これに対し、第２表中において＊印で示す条件が本発明
範囲から外れた比較法では、いずれも伸びが大きな値を
示していないことが明らかである。On the other hand, it is clear that none of the comparative methods in which the conditions marked with * in Table 2 are outside the scope of the present invention exhibit large elongation values.
災胤拠主
前出の第１表に示される各種成分組成の二相ステンレス
鋼粉を内径２０鰭の金型内にワックス系バインダと共に
圧粉化し、外径２０ｍ、高さ２００の圧粉体を得た。こ
の圧粉体の密度は理論密度の約７５％であった。得られ
た圧粉体をいずれも真空炉にて１０００℃、２０分の焼
結を行った。焼結体の密度は７５〜８５％の範囲であっ
た。得られた焼結体を用いて、第１図に示す装置におい
て自由鍛造加工を行った。下型１２を固定しておき、上
型１４を周囲のガイド１６に沿って落下させて成形をお
こなった。上下の型を取り巻いて、適宜発熱体を設ける
ことにより、図示の素材は所定温度に常に加熱される。Duplex stainless steel powders having various compositions shown in Table 1 above are compacted together with a wax binder in a mold with an inner diameter of 20 fins to form a compact with an outer diameter of 20 m and a height of 200 m. I got it. The density of this compact was approximately 75% of the theoretical density. All of the obtained compacts were sintered in a vacuum furnace at 1000°C for 20 minutes. The density of the sintered body was in the range of 75-85%. Using the obtained sintered body, free forging was performed in the apparatus shown in FIG. Molding was performed by keeping the lower mold 12 fixed and dropping the upper mold 14 along the surrounding guide 16. By appropriately providing heating elements surrounding the upper and lower molds, the illustrated material is constantly heated to a predetermined temperature.
使用した金型はＮｉ基の耐熱合金で製作し、発熱体を設
けて等部下で加工できるようにした。加工はＮ２＋アル
ゴンガス中で行い、素材にはガラス系潤滑剤を使用した
。The mold used was made of a Ni-based heat-resistant alloy, and a heating element was installed to enable processing under uniform conditions. The processing was performed in N2 + argon gas, and a glass-based lubricant was used for the material.
各種の温度および歪速度で加工した結果は第３表に示す
とおりであった。ここで歪速度εとは、上型の降下速度
ｖ（ａｍ八へｃ）と素材高さｈ（ｉｓ）より、ε＝Ｉｎ
（ｖ／ｈ）で計算される値である。The results of processing at various temperatures and strain rates are shown in Table 3. Here, the strain rate ε is defined as ε=In
(v/h).
なお、第３表における加工荷重とは、素材高さが半分（
ｈ、／２）になった時の加工荷重を言う。Note that the machining load in Table 3 is when the material height is half (
h, /2).
第２図はアトマイズ粉末の圧粉化と焼結により得た粉末
材の自由鍛造における圧下変位と荷重の関係を示してい
る。素材の初期高さはｈｏ、歪速度は９ ｘｌｏ−″（
１／５ｅｃ）であった。アの領域で素材密度が上昇し、
密度がほとんど１００％になってから接触面積にほぼ比
例して荷重が上昇するのが分かる。Figure 2 shows the relationship between rolling displacement and load in free forging of powder material obtained by compacting and sintering atomized powder. The initial height of the material is ho, the strain rate is 9xlo-'' (
1/5 ec). The material density increases in the region of
It can be seen that the load increases almost in proportion to the contact area after the density reaches almost 100%.
第３図は溶製材の自由鍛造の場合を示す第２図と同様の
図面であり、圧下と共に荷重が急激に上昇する。この場
合、素材の初期高さはｈｏ、歪速度は１０ （１／５ｅ
ｅ）であった。FIG. 3 is a drawing similar to FIG. 2 showing the case of free forging of ingot material, and the load increases rapidly with rolling reduction. In this case, the initial height of the material is ho, and the strain rate is 10 (1/5e
e).
第３表に示す結果からも明らかなように、本発明によれ
ば、９００〜１０５０℃と比較的低い温度でのしかも著
しく低荷重の加工が可能となることが分かる。As is clear from the results shown in Table 3, it can be seen that according to the present invention, processing can be performed at a relatively low temperature of 900 to 1050°C and with a significantly low load.
第１表 （！！！量％）
第２表
＊：本発明の範囲外
第３表
（発明の効果）
以上説明してきたように、本発明にかかる二相系ステン
レス鋼のアトマイズ鋼粉を用いた超塑性加工法において
は、従来法と比較し、加工に要する荷重が著しく低く、
小さな荷重で大型品、複雑形状品の加工が可能となる。Table 1 (!!! Amount %) Table 2 *: Outside the scope of the present invention Table 3 (Effects of the invention) As explained above, the atomized steel powder of the duplex stainless steel according to the present invention is used. In the superplastic processing method, the load required for processing is significantly lower than that of conventional methods.
It is possible to process large products and complex-shaped products with a small load.
一方では、加工温度を低くすることが可能で、型費用が
少なくてすむばかりでなく、結晶粒の成長を阻止できる
ことから、製品品質の向上につながる。On the other hand, it is possible to lower the processing temperature, which not only reduces mold costs, but also prevents the growth of crystal grains, leading to improved product quality.
また、上記の加工条件と同等の温度範囲、歪速度で二相
系ステンレス鋼の鋼粉の押出加工を行ったところ、低荷
重において従来品と同等の製品を得ることができた。Furthermore, when we extruded duplex stainless steel powder under the same temperature range and strain rate as the above processing conditions, we were able to obtain a product equivalent to the conventional product under low load.
第１図は、実施例で使用した焼結体の自由鍛造装置の概
念図、
第２図は、本発明にかかる粉末材の自由鍛造における圧
下変位と荷重との関係を示すグラフ、および
第３図は、従来の溶製材の自由鍛造における圧下変位と
荷重との関係を示すグラフである。FIG. 1 is a conceptual diagram of the free forging apparatus for sintered compacts used in the examples, FIG. 2 is a graph showing the relationship between rolling displacement and load in free forging of powder material according to the present invention, and FIG. The figure is a graph showing the relationship between rolling displacement and load in conventional free forging of ingot material.
Claims (6)
てＭｏ、Ｎを含有する、常温付近でフェライト相とオー
ステナイト相の二相組織を呈する二相ステンレス鋼系ア
トマイズ鋼粉の集合体を、７００℃以上、（（フェライ
ト単相となる温度）−１００℃）以下の温度域で、１×
１０＾−＾６１／ｓｅｃ以上、１×１０＾０１／ｓｅｃ
以下の歪速度で変形させることを特徴とする、二相ステ
ンレス鋼粉の熱間加工方法。(1) An aggregate of duplex stainless steel atomized steel powder that exhibits a two-phase structure of ferrite phase and austenite phase near room temperature, containing Fe, Cr, and Ni as main components, and containing Mo and N as necessary. , 1× in the temperature range of 700°C or higher and ((temperature at which ferrite becomes single phase) -100°C) or lower
10^-^61/sec or more, 1×10^01/sec
A method for hot working duplex stainless steel powder, characterized by deforming it at the following strain rate:
．０〜３５．０％、Ｎｉ：３．０〜１８．０％、残部Ｆ
ｅおよび付随不純物 から成る鋼組成を有する、特許請求の範囲第１項記載の
方法。(2) The duplex stainless steel has Cr: 12% by weight.
．． 0-35.0%, Ni: 3.0-18.0%, balance F
2. The method of claim 1, having a steel composition consisting of e and incidental impurities.
．０〜３５．０％、Ｎｉ：３．０〜１８．０％、Ｃ：０
．０５％以下、Ｓｉ：０．０５〜５．０％、Ｍｎ：０．
０５〜８．０％、Ｍｏ：５．０％以下、Ｎ：０．０５〜
０．８％、Ｃｕ：０．８％以下、Ｐ：０．０５％以下、
Ｓ：０．００５％以下、残部Ｆｅおよび付随不純物 から成る鋼組成を有する、特許請求の範囲第１項記載の
方法。(3) The duplex stainless steel has Cr: 12% by weight.
．． 0-35.0%, Ni: 3.0-18.0%, C: 0
．． 05% or less, Si: 0.05 to 5.0%, Mn: 0.
05~8.0%, Mo: 5.0% or less, N: 0.05~
0.8%, Cu: 0.8% or less, P: 0.05% or less,
The method according to claim 1, wherein the steel composition comprises S: 0.005% or less, the balance consisting of Fe and incidental impurities.
フェライト相とオーステナイト相の二相組織を呈する二
相ステンレス鋼系アトマイズ鋼粉を、熱間静水圧プレス
装置において、７００℃以上、〔（フェライト単相とな
る温度）−１００℃〕以下の温度域で、１×１０＾−＾
６１／ｓｅｃ以上、１×１０＾０１／ｓｅｃ以下の歪速
度で変形・緻密化させることを特徴とする、二相ステン
レス鋼粉の熱間静水圧加工方法。(4) Duplex stainless steel atomized steel powder containing Fe, Cr, and Ni as main components and exhibiting a two-phase structure of ferrite and austenite phases at around room temperature was heated at 700°C or higher in a hot isostatic press machine. (Temperature at which ferrite becomes single phase) -100℃] In the temperature range below, 1 x 10^-^
A hot isostatic processing method for duplex stainless steel powder, characterized by deforming and densifying it at a strain rate of 61/sec or more and 1×10^01/sec or less.
．０〜３５．０％、Ｎｉ：３．０〜１８．０％、残部Ｆ
ｅおよび付随不純物 から成る鋼組成を有する、特許請求の範囲第４項記載の
方法。(5) The duplex stainless steel has Cr: 12% by weight.
．． 0-35.0%, Ni: 3.0-18.0%, balance F
5. The method of claim 4, having a steel composition consisting of e and incidental impurities.
．０〜３５．０％、Ｎｉ：３．０〜１８．０％、Ｃ：０
．０５％以下、Ｓｉ：０．０５〜５．０％、Ｍｎ：０．
０５〜８．０％、Ｍｏ：５．０％以下、Ｎ：０．０５〜
０．８％、Ｃｕ：０．８％以下、Ｐ：０．０５％以下、
Ｓ：０．００５％以下、残部Ｆｅおよび付随不純物 から成る鋼組成を有する、特許請求の範囲第４項記載の
方法。(6) The duplex stainless steel has Cr: 12% by weight.
．． 0-35.0%, Ni: 3.0-18.0%, C: 0
．． 05% or less, Si: 0.05 to 5.0%, Mn: 0.
05~8.0%, Mo: 5.0% or less, N: 0.05~
0.8%, Cu: 0.8% or less, P: 0.05% or less,
The method according to claim 4, wherein the steel composition comprises S: 0.005% or less, the balance being Fe and incidental impurities.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6547786A JPS62222044A (en) | 1986-03-24 | 1986-03-24 | Hot-working method for two-phase stainless steel powder |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6547786A JPS62222044A (en) | 1986-03-24 | 1986-03-24 | Hot-working method for two-phase stainless steel powder |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS62222044A true JPS62222044A (en) | 1987-09-30 |
Family
ID=13288219
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6547786A Pending JPS62222044A (en) | 1986-03-24 | 1986-03-24 | Hot-working method for two-phase stainless steel powder |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62222044A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01225754A (en) * | 1988-02-04 | 1989-09-08 | Armco Advanced Materials Corp | Double molten high manganese stainless steel |
| JP2010138455A (en) * | 2008-12-11 | 2010-06-24 | Diamet:Kk | Stainless steel sintered compact and manufacturing method thereof |
| US20160319405A1 (en) * | 2013-12-27 | 2016-11-03 | Sandvik Intellectual Property Ab | Corrosion resistant duplex steel alloy, objects made thereof, and method of making the alloy |
| CN112063919A (en) * | 2020-07-31 | 2020-12-11 | 丽水市正阳电力设计院有限公司 | Duplex stainless steel |
-
1986
- 1986-03-24 JP JP6547786A patent/JPS62222044A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH01225754A (en) * | 1988-02-04 | 1989-09-08 | Armco Advanced Materials Corp | Double molten high manganese stainless steel |
| JP2010138455A (en) * | 2008-12-11 | 2010-06-24 | Diamet:Kk | Stainless steel sintered compact and manufacturing method thereof |
| US20160319405A1 (en) * | 2013-12-27 | 2016-11-03 | Sandvik Intellectual Property Ab | Corrosion resistant duplex steel alloy, objects made thereof, and method of making the alloy |
| 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 |
| CN112063919A (en) * | 2020-07-31 | 2020-12-11 | 丽水市正阳电力设计院有限公司 | Duplex stainless steel |
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