JPH0570835A - Manufacture of duplex stainless steel sheet extremely small in roughening of surface caused by superplastic forming - Google Patents
Manufacture of duplex stainless steel sheet extremely small in roughening of surface caused by superplastic formingInfo
- Publication number
- JPH0570835A JPH0570835A JP25963891A JP25963891A JPH0570835A JP H0570835 A JPH0570835 A JP H0570835A JP 25963891 A JP25963891 A JP 25963891A JP 25963891 A JP25963891 A JP 25963891A JP H0570835 A JPH0570835 A JP H0570835A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- duplex stainless
- superplastic forming
- steel sheet
- roughening
- 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.)
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、超塑性成形を行った
場合にローピングに似た肌荒れが生ずることの極めて少
ない２相ステンレス鋼板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 a duplex stainless steel sheet which is extremely free from roughening similar to roping when superplastic forming is performed.
【０００２】[0002]
【従来の技術】一般に、２相ステンレス鋼板は超塑性を
示すことが知られている。例えば、特開60-75524号公報
には、強制冷却および冷間で総圧下率20％以上のクロス
圧延を施すことことにより異方性の生じにくい２相ステ
ンレス鋼板の製造方法が記載されており、また、特公平
2-4656号公報には、特定成分範囲の２相ステンレス鋼鋳
造スラブを、熱間圧延後直ちに急冷し、次いで前記熱間
圧延方向とは異なる向きで、総圧下率30％以上の冷間圧
延を行うことにより２相ステンレス鋼板を製造する方法
が記載されている。2. Description of the Related Art It is generally known that duplex stainless steel sheets exhibit superplasticity. For example, Japanese Unexamined Patent Publication No. 60-75524 describes a method for producing a duplex stainless steel sheet in which anisotropy is less likely to occur by performing forced cooling and cold rolling at a total reduction of 20% or more. , Also fair
No. 2-4656 discloses that a duplex stainless steel cast slab having a specific component range is rapidly cooled immediately after hot rolling, and then cold rolled in a direction different from the hot rolling direction with a total reduction of 30% or more. The method for producing a duplex stainless steel sheet by carrying out is described.
【０００３】[0003]
【発明が解決しようとする課題】しかしながら、前記従
来技術で製造された２相ステンレス鋼板は、これを超塑
性成形すると、超塑性成形時にいずれもローピングに似
た肌荒れが発生し、用途によってはこの状態では製品に
できず、これを製品とするためには、後工程の研磨にて
除去する必要があるが、通常の研磨工程でこの肌荒れを
完全に除去するには多大の労力と時間を必要とするなど
の課題があった。However, the superplastic forming of the duplex stainless steel sheets manufactured by the above-mentioned prior art causes roughening similar to roping during superplastic forming, and depending on the application, It cannot be made into a product in the state, and in order to make it a product, it needs to be removed by polishing in a post process, but it takes a lot of labor and time to completely remove this rough skin in the normal polishing process. There was a problem such as
【０００４】この肌荒れ現象は、従来は超塑性成形時に
生ずる酸化膜に覆われているため、それを確認すること
はできなかったが、その膜を酸洗および研磨にて除去し
たところ、肌荒れが顕著に現われていることを発見した
のである。[0004] This rough skin phenomenon could not be confirmed because it was conventionally covered with an oxide film generated during superplastic forming, but when the film was removed by pickling and polishing, rough skin was found. It was discovered that it appeared remarkably.
【０００５】[0005]
【課題を解決するための手段】そこで、本発明者等は、
超塑性成形しても前記ローピングに似た肌荒れが発生し
ない２相ステンレス鋼板を開発すべく研究を行った結
果、前記超塑性成形時に発生するローピングに似た肌荒
れは、熱間圧延方向と平行に生ずることろから、熱間圧
延条件に関係があり、前記熱間圧延温度を１２５０℃以
上、好ましくは１２５０〜１３００℃とすることにより
超塑性成形を行った場合にローピングに似た肌荒れが生
ずることの極めて少ない２相ステンレス鋼が得られる、
という知見を得たのである。Therefore, the present inventors have
As a result of research to develop a duplex stainless steel sheet that does not cause roughening similar to roping even when superplastic forming, roughening similar to roping that occurs during superplastic forming is parallel to the hot rolling direction. From what happens, it depends on the hot rolling conditions, and when the hot rolling temperature is 1250 ° C. or higher, preferably 1250 to 1300 ° C., roughening similar to roping occurs when superplastic forming is performed. It is possible to obtain duplex stainless steel with very little
I got the knowledge that.
【０００６】この発明は、かかる知見にもとずいてなさ
れたものであって、Ｃ：０．０２重量％以下、Ｓｉ：
２．０重量％以下、Ｍｎ：３．０重量％以下、Ｎｉ：３
〜１０重量％、Ｃｒ：２０〜３５重量％、Ｍｏ：０．５
〜６．０重量％、Ｎ：０．０８〜０．３重量％を含有
し、残部：Ｆｅおよび不可避不純物からなる２相ステン
レス鋼鋳造スラブを、温度：１２５０℃以上で熱間圧延
を行い、次いで前記熱間圧延方向と異なる方向に、圧延
率70％以上の冷間圧延を施す超塑性成形による肌荒れの
極めて少ない２相ステンレス鋼板の製造方法、に特徴を
有するものである。The present invention has been made on the basis of such findings, and C: 0.02% by weight or less, Si:
2.0 wt% or less, Mn: 3.0 wt% or less, Ni: 3
-10 wt%, Cr: 20-35 wt%, Mo: 0.5
~ 6.0 wt%, N: 0.08-0.3 wt%, the balance: Fe and unavoidable impurities duplex stainless steel cast slab hot-rolled at a temperature of 1250 ℃ or more, Next, a method for producing a two-phase stainless steel sheet with extremely little rough skin by superplastic forming, which is performed by cold rolling at a rolling rate of 70% or more in a direction different from the hot rolling direction, is characterized.
【０００７】次に、この発明にかかる２相ステンレス鋼
の成分組成を前記のごとく限定した理由を説明する。Next, the reason why the composition of the duplex stainless steel according to the present invention is limited as described above will be explained.
【０００８】（ａ）Ｃ Ｃは0.02％より多いと粒界腐食が発生し、耐孔食性が劣
化し、炭化物の析出により熱間加工性が低下し、かつγ
相が高温域まで安定に存在し、高温での熱間加工性が低
下し、そして炭化物は超塑性変形中にキャビテーション
発生の起点となるため0.02％以下にする必要があり、0.
01％以下がより好ましい。(A) CC If C is more than 0.02%, intergranular corrosion occurs, pitting corrosion resistance deteriorates, hot workability deteriorates due to precipitation of carbides, and γ
The phase is stable up to a high temperature range, the hot workability at high temperature deteriorates, and carbide is the starting point of cavitation during superplastic deformation, so it must be 0.02% or less, 0.
01% or less is more preferable.
【０００９】（ｂ）Ｓｉ Ｓｉは、耐蝕性の向上に有効であるが、２．０％より多
いと、高温でα相の粒成長による脆化、γ相による脆
化、および４７５℃脆性に悪影響を与えるので、2.0 ％
以下にする必要があり、1.0 ％以下がより好ましい。(B) Si Si is effective in improving the corrosion resistance, but if it is more than 2.0%, it becomes brittle due to grain growth of α phase, brittleness due to γ phase, and 475 ° C. brittleness at high temperature. 2.0% because it has a negative effect
It is necessary to make it below, and more preferably 1.0% or less.
【００１０】（ｃ）Ｍｎ Ｍｎは、3.0 ％より多いと耐食性が劣化し、γ相量が必
要以上に増加する。また製鋼工程中に混入される元素で
あって通常のフェライトまたはオーステナイトステンレ
ス鋼の成分範囲である3.0 ％以下の範囲内に限定すると
工業的に製造し得るからである。(C) Mn If Mn is more than 3.0%, the corrosion resistance deteriorates and the amount of γ phase increases more than necessary. Further, it is because it is an element that is mixed in during the steelmaking process, and if it is limited to the range of 3.0% or less which is the composition range of ordinary ferrite or austenitic stainless steel, it can be industrially produced.
【００１１】（ｄ）Ｎｉ Ｎｉは、オーステナイト形成元素であり、Ｎｉが３％よ
り少ないとγ相が消失し、超塑性性能を劣化し、一方、
１０％より多いと粗大な必要量以上のγ相が発生するば
かりでなく製造コストが上昇するのでＮｉは３〜１０％
の範囲にする必要がある。(D) Ni Ni is an austenite forming element, and when Ni is less than 3%, the γ phase disappears and the superplastic performance deteriorates.
If it is more than 10%, not only a large amount of γ phase is produced, but also the manufacturing cost rises.
Must be in the range.
【００１２】（ｅ）Ｃｒ Ｃｒはフェライト形成元素であり、Ｃｒが２０％より少
ないと耐食性が劣化し、一方、３５％より多いと靭性が
劣化する。したがって、Ｃｒは２０〜３５％の範囲内に
する必要があり、２３〜２７％の範囲内がより好まし
い。(E) Cr Cr is a ferrite forming element, and if Cr is less than 20%, corrosion resistance deteriorates, while if it exceeds 35%, toughness deteriorates. Therefore, Cr needs to be in the range of 20 to 35%, and more preferably in the range of 23 to 27%.
【００１３】（ｆ）Ｍｏ Ｍｏはフェライト形成元素であり、Ｍｏが0.5 ％より少
ないと耐局部腐食性が劣化し、優れた超塑性変形能に深
く関係しているγ相が得にくく、一方、6.0 ％より多い
と靭性の劣化および耐局部腐食性が劣化するばかりでな
く製造コストが上昇するのでＭｏは0.５〜6.0 ％の範囲
内にする必要があり、１〜４％の範囲内がより好まし
い。(F) Mo Mo is a ferrite forming element, and if Mo is less than 0.5%, the local corrosion resistance deteriorates and it is difficult to obtain the γ phase which is closely related to excellent superplastic deformability. If it is more than 6.0%, not only the toughness and local corrosion resistance deteriorate but also the manufacturing cost rises, so Mo must be in the range of 0.5 to 6.0%, and the range of 1 to 4% is recommended. More preferable.
【００１４】（ｇ）Ｎ Ｎは、Ｃと同様な強力なオーステナイト形成元素であ
り、このためＮ含有量は他のオーステナイト形成元素お
よびフェライト形成元素とのバランスで定める。またＮ
はγ相に多く固溶して耐孔食性を向上するに有効な元素
である。Ｎ量の増加とともに耐孔食性は向上するので、
少なくとも0.08％以上必要とし、一方、Ｎが0.3 ％より
多いとブローホールなど鋼塊の欠陥を生じたりγ相が安
定に存在することにより熱間加工性が劣化するので、0.
08〜０.3％の範囲内にする必要があり、より好ましい範
囲は0.08〜０.14 ％である。(G) N N is a strong austenite-forming element similar to C. Therefore, the N content is determined by the balance with other austenite-forming elements and ferrite-forming elements. Also N
Is an element effective in improving the pitting corrosion resistance by forming a solid solution in the γ phase. Since the pitting corrosion resistance improves as the N content increases,
At least 0.08% or more is required. On the other hand, if N is more than 0.3%, hot workability deteriorates due to defects such as blowholes in the steel ingot and stable existence of the γ phase.
It should be in the range of 08 to 0.3%, and the more preferable range is 0.08 to 0.14%.
【００１５】（ｈ）熱間圧延 超塑性成形時に発生するローピングに似た肌荒れは、熱
間圧延方向と平行に生ずることろから、熱間圧延条件に
関係があり、１２５０℃以上の高温に加熱することによ
り、フェライト相量を多くし、その後の熱間圧延により
微細なオーステナイト相を析出させることが超塑性成形
時に生ずるローピングに似た肌荒れの発生を低減させる
ことができる。したがって、前記熱間圧延温度を１２５
０℃以上と定めた。(H) Hot rolling Since roughening similar to roping that occurs during superplastic forming occurs in parallel with the hot rolling direction, it is related to hot rolling conditions and heated to a high temperature of 1250 ° C. or higher. By doing so, increasing the amount of ferrite phase and precipitating a fine austenite phase by subsequent hot rolling can reduce the occurrence of roughening similar to roping that occurs during superplastic forming. Therefore, the hot rolling temperature is set to 125
It was determined to be 0 ° C or higher.
【００１６】（ｉ）冷間圧延 冷間圧延は、熱間圧延の影響をなくすために、常にこの
熱間圧延方向とは異なる方向に冷間圧延を行われるが、
その圧延率が７０％未満では熱間圧延の影響を十分にな
くすことができないところから、冷間圧延の圧延率は７
０％以上と定めた。(I) Cold rolling In cold rolling, cold rolling is always carried out in a direction different from the hot rolling direction in order to eliminate the influence of hot rolling.
If the rolling rate is less than 70%, the effect of hot rolling cannot be sufficiently eliminated, so the rolling rate of cold rolling is 7%.
It was set at 0% or more.
【００１７】この発明の方法で製造された２相ステンレ
ス鋼は、いかなる条件で超塑性成形を行ってもローピン
グに似た肌荒れを生ずることは少ないが、とくに超塑性
成形を温度：９５０〜１０５０℃の範囲内で行うと、超
塑性成形時に発生する肌荒れが極めて少ないところから
超塑性成形温度は９５０〜１０５０℃であることが好ま
しく、特に９７５〜１０５０℃であることが一層好まし
い。The duplex stainless steel produced by the method of the present invention rarely causes roughening similar to roping under any condition of superplastic forming. However, superplastic forming is performed at a temperature of 950 to 1050 ° C. When the temperature is within the range, the superplastic forming temperature is preferably 950 to 1050 ° C., and more preferably 975 to 1050 ° C., since the surface roughness generated during superplastic forming is extremely small.
【００１８】[0018]
【実施例】表１に示す成分組成(SUS329J2L) の２相ステ
ンレス鋼を溶解し、鋳造してスラブを用意した。表１に
おける単位は重量％である。[Example] A slab was prepared by melting a two-phase stainless steel having the composition (SUS329J2L) shown in Table 1 and casting it. The unit in Table 1 is% by weight.
【００１９】[0019]
【表１】 [Table 1]
【００２０】前記表１に示す成分組成の２相ステンレス
鋼スラブを表２に示される温度で熱間圧延し、その後直
ちに急冷し、次いで前記熱間圧延方向と直角方向に表２
に示される圧延率で冷間圧延を施し、本発明法１〜７お
よび比較法１〜３を実施した。 なお、比較法１は従来
法でもあり、この発明の条件から外れた値に※印を付し
て示した。A duplex stainless steel slab having the composition shown in Table 1 was hot-rolled at a temperature shown in Table 2, immediately followed by quenching, and then in a direction perpendicular to the hot-rolling direction.
Cold rolling was carried out at the rolling rate shown in Table 1, and the methods 1 to 7 of the present invention and the comparative methods 1 to 3 were carried out. Comparative method 1 is also a conventional method, and values deviating from the conditions of the present invention are marked with *.
【００２１】この様にして得られた２相ステンレス鋼板
を直径：６０ｍｍの円板に加工して加工素材を作製し、
この加工素材を表２に示される温度に加熱し、高さ40mm
までガス圧を掛け、ドーム超塑性成形を行った。超塑性
成形後のドーム材料表面を軽く研磨し、ついで、酸化被
膜を除去後目視により肌荒れを観察し、評価し、その結
果を表２に示した。The duplex stainless steel plate thus obtained is processed into a disk having a diameter of 60 mm to prepare a processing material,
This processed material is heated to the temperature shown in Table 2 and the height is 40mm.
Gas pressure was applied up to and dome superplastic forming was performed. The surface of the dome material after superplastic forming was lightly polished, and after removing the oxide film, the rough surface was visually observed and evaluated, and the results are shown in Table 2.
【００２２】前記評価基準は、 Ａ：ほとんど肌荒れは認められない、 Ｂ：実用上問題のない程度の僅かな肌荒れあり、 Ｃ：実用上問題のある肌荒れあり、 Ｄ：明らかに肌荒れが認められ問題あり の４段階評価とした。The evaluation criteria are as follows: A: Almost no rough skin is observed, B: Slight rough skin without practical problems, C: Rough skin with practical problems, D: Clearly rough skin is recognized There was a four-level evaluation.
【００２３】[0023]
【表２】 [Table 2]
【００２４】[0024]
【発明の効果】表２に示される結果から、本発明法１〜
７の熱間圧延を温度１２５０℃以上で行い、前記熱間圧
延方向と直角方向に圧延率：70％以上の冷間圧延を施す
ことにより得られた２相ステンレス鋼板を、温度：９５
０〜１０５０℃で超塑性成形を行ったものは、肌荒れが
殆ど認められないかまたは認められても実用上問題のな
い評価が得られている。From the results shown in Table 2, the method of the present invention 1 to
The hot rolling of No. 7 was carried out at a temperature of 1250 ° C. or higher, and the duplex stainless steel sheet obtained by cold rolling at a rolling ratio of 70% or more in the direction perpendicular to the hot rolling direction was used.
Those subjected to superplastic forming at 0 to 1050 ° C. have almost no skin roughness, or have been evaluated practically without problems even if they are recognized.
【００２５】これに対し比較法１の温度１２５０℃未満
の熱間圧延および70％未満の冷間圧延圧延率で得られた
２相ステンレス鋼板を温度：９５０℃で超塑性成形を行
ったものは肌荒れが激しく問題があり、さらに、比較法
２の温度１２５０℃未満の熱間圧延および70％以上の冷
間圧延圧延率で得られた２相ステンレス鋼板および比較
法３の温度１２５０℃以上の熱間圧延および70％未満の
冷間圧延圧延率で得られた２相ステンレス鋼板を温度：
１０５０℃で超塑性成形を行っても肌荒れは改善でき
ず、実用上問題があることが分かる。On the other hand, the two-phase stainless steel sheets obtained by the hot rolling at a temperature of less than 1250 ° C. and the cold rolling reduction rate of less than 70% of Comparative Method 1 were superplastically formed at a temperature of 950 ° C. There is a serious problem of rough skin, and a duplex stainless steel sheet obtained by hot rolling at a temperature of less than 1250 ° C and a cold rolling reduction rate of 70% or more in Comparative Method 2 and heat at a temperature of 1250 ° C or more in Comparative Method 3 are obtained. Temperature of a duplex stainless steel sheet obtained by hot rolling and cold rolling reduction of less than 70%:
Even if superplastic forming is carried out at 1050 ° C., the rough skin cannot be improved, and it is understood that there is a problem in practical use.
【００２６】この発明によれば、肌荒れの少ない超塑性
成形が可能になり、後工程の負担を軽減することがで
き、工業上非常に有益な成形品を得ることができる。According to the present invention, superplastic forming with less rough skin is possible, the burden of the post-process can be reduced, and a molded product which is very useful in industry can be obtained.
Claims (1)
重量％以下、Ｍｎ：３．０重量％以下、Ｎｉ：３〜１０
重量％、Ｃｒ：２０〜３５重量％、Ｍｏ：０．５〜６．
０重量％、Ｎ：０．０８〜０．３重量％を含有し、残
部：Ｆｅおよび不可避不純物からなる２相ステンレス鋼
鋳造スラブを、温度：１２５０℃以上で熱間圧延し、次
いで前記熱間圧延方向と異なる方向に、圧延率70％以上
の冷間圧延を施すことを特徴とする超塑性成形による肌
荒れの極めて少ない２相ステンレス鋼板の製造方法。1. C: 0.02 wt% or less, Si: 2.0
% By weight, Mn: 3.0% by weight or less, Ni: 3 to 10
% By weight, Cr: 20-35% by weight, Mo: 0.5-6.
A two-phase stainless steel cast slab containing 0 wt% and N: 0.08 to 0.3 wt% and the balance: Fe and unavoidable impurities was hot-rolled at a temperature of 1250 ° C. or higher, and then hot-rolled. A method for producing a duplex stainless steel sheet with extremely low surface roughness by superplastic forming, which comprises performing cold rolling at a rolling rate of 70% or more in a direction different from the rolling direction.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25963891A JPH08933B2 (en) | 1991-09-11 | 1991-09-11 | Method for producing duplex stainless steel sheet with extremely low surface roughness by superplastic forming |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25963891A JPH08933B2 (en) | 1991-09-11 | 1991-09-11 | Method for producing duplex stainless steel sheet with extremely low surface roughness by superplastic forming |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0570835A true JPH0570835A (en) | 1993-03-23 |
| JPH08933B2 JPH08933B2 (en) | 1996-01-10 |
Family
ID=17336842
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP25963891A Expired - Lifetime JPH08933B2 (en) | 1991-09-11 | 1991-09-11 | Method for producing duplex stainless steel sheet with extremely low surface roughness by superplastic forming |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH08933B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06330250A (en) * | 1993-05-20 | 1994-11-29 | Nippon Yakin Kogyo Co Ltd | Formed part of hand print or the like having fine ruggedness and its production |
| FR2741360A1 (en) * | 1995-11-08 | 1997-05-23 | Nippon Yakin Kogyo Co Ltd | TWO-PHASE SUPERPLASTIC STAINLESS STEEL HAVING LOW DEFORMATION RESISTANCE AND EXCELLENT LENGTH PROPERTIES |
| US5672315A (en) * | 1995-11-03 | 1997-09-30 | Nippon Yakin Kogyo Co., Ltd. | Superplastic dual-phase stainless steels having a small deformation resistance and excellent elongation properties |
-
1991
- 1991-09-11 JP JP25963891A patent/JPH08933B2/en not_active Expired - Lifetime
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06330250A (en) * | 1993-05-20 | 1994-11-29 | Nippon Yakin Kogyo Co Ltd | Formed part of hand print or the like having fine ruggedness and its production |
| US5672315A (en) * | 1995-11-03 | 1997-09-30 | Nippon Yakin Kogyo Co., Ltd. | Superplastic dual-phase stainless steels having a small deformation resistance and excellent elongation properties |
| FR2741360A1 (en) * | 1995-11-08 | 1997-05-23 | Nippon Yakin Kogyo Co Ltd | TWO-PHASE SUPERPLASTIC STAINLESS STEEL HAVING LOW DEFORMATION RESISTANCE AND EXCELLENT LENGTH PROPERTIES |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH08933B2 (en) | 1996-01-10 |
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