JPS60262946A - Two-phase stainless steel with superior hot workability - Google Patents
Two-phase stainless steel with superior hot workabilityInfo
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- JPS60262946A JPS60262946A JP11955084A JP11955084A JPS60262946A JP S60262946 A JPS60262946 A JP S60262946A JP 11955084 A JP11955084 A JP 11955084A JP 11955084 A JP11955084 A JP 11955084A JP S60262946 A JPS60262946 A JP S60262946A
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Abstract
Description
【発明の詳細な説明】
技術分野
二相ステンレス鋼に関して、この明細書に述べる技術内
容は、その成分組成に工夫を加えることによって、熱間
加工性の向上を図ることに関連している〇
背景技術
二相ステンレス鋼は、オーステナイト系ステンレス鋼や
フェライト系ステンレス鋼に較べて、耐食性や耐応力腐
食割れ抵抗性および溶接性に優れていることから、近年
、構造用材料として幅広く用いられるようになシ、最近
では、COBやH,Sを含む環境下でのパイプライン用
鋼として注目されている〇
しかしながら二相ステンレス鋼は、フェライト相とオー
ステナイト相から成っているため、熱間加工の際に、そ
れらの界面に割れが生じ易く、従つて分塊圧延や熱間圧
延における歩留りが極めて悪いところに問題を残してい
た・
発明の目的
この発明は、上記の問題を有利に解決するもので、分塊
圧延や熱間圧延時における割れ発生を極力低減して歩留
りの向上を可能ならしめた、熱間加工性1優れた二相ス
テンレス鋼を提案することを目的とする。[Detailed Description of the Invention] Technical Field The technical content described in this specification regarding duplex stainless steel is related to improving hot workability by modifying its component composition〇Background Technology Duplex stainless steel has been widely used as a structural material in recent years because it has superior corrosion resistance, stress corrosion cracking resistance, and weldability compared to austenitic stainless steel and ferritic stainless steel. Recently, it has been attracting attention as a steel for pipelines in environments containing COB, H, and S.However, since duplex stainless steel consists of a ferrite phase and an austenite phase, it is difficult to use during hot working. , cracks are likely to occur at their interfaces, resulting in extremely low yields during blooming and hot rolling.Purpose of the InventionThe present invention advantageously solves the above problems. The purpose of the present invention is to propose a duplex stainless steel with excellent hot workability 1, which makes it possible to improve the yield by minimizing the occurrence of cracks during blooming and hot rolling.
解決手段の解明経緯
高温でフェライト相とオーステナイト相との二相組織を
呈するステンレス鋼の熱間加工性については、これまで
にも数多くの研究がなされていて、その一般的な向上策
としては、Sを低減すること、ならびにさらにREMを
添加することなどが有効であるといわれている。Elucidation of the solution A large number of studies have been conducted on the hot workability of stainless steel, which exhibits a two-phase structure of ferrite and austenite phases at high temperatures, and general measures to improve it include: It is said that reducing S and further adding REM are effective.
そこで発明者らも、まず鋼中Sの低減による改善を試み
、Sを0.0016重量%(以下単に係で示す)未満に
低減し次二相ステンレス鋼スラブを連続鋳造で製造し、
分塊圧延ミルでサイジング後、熱間圧延を施したところ
、熱延板の両端部には、板幅方向に約705+の長さを
もった割れがいたるところに発止した。Therefore, the inventors first tried to improve the S content in the steel by reducing the S content to less than 0.0016% by weight (hereinafter referred to simply as "Substance"), and then produced a duplex stainless steel slab by continuous casting.
After sizing with a blooming mill and hot rolling, cracks with a length of about 705+ in the width direction of the hot-rolled sheet appeared everywhere on both ends of the hot-rolled sheet.
そこで次に、従来いわれているRIMの効能を検討すべ
く、Sが0.0016係未満でかつRIM 1に0.0
15%含む二相ステンレス鋼のインゴットを造り、上述
と同様の実駿に供した。その結果、熱延板における耳割
れの発生は軽微となったが、表面性状はREM無添加の
ものに比べてかえって悪化した0さらに、かかるRIM
添加鋼は、連続鋳造法を適用することができず、インゴ
ツト材とする必要がおることから、この発明で所期した
歩留りの向上はあまり望み得ないことも判明した。Therefore, in order to examine the efficacy of RIM, which has been conventionally said, we decided to
An ingot of duplex stainless steel containing 15% was made and subjected to the same experiment as described above. As a result, the occurrence of edge cracking in the hot-rolled sheet was slight, but the surface quality was worse than that of the REM-free sheet.
It has also been found that the improvement in yield as expected by the present invention cannot be expected much because the continuous casting method cannot be applied to additive steel and it is necessary to make it into an ingot material.
この発明は、上記の諸問題を有利に解決して、たとえ割
れの発生し易い連続鋳造材を素材とした場合であっても
、耳割れなどの発生を極力低減して、歩留りの大幅な向
上を実現したものであり・二相ステンレス鋼の組成につ
き、とくにAI!を一定範囲に限定した上で、Sを低減
すると共に、こ°のSiに応じてOaを添加することが
、所期した目的の達成に関し、極めて有効であるとの新
規知見に立脚する0
発明の構成
すなわち仁の発明性、a : o、oa%以下、Sにs
、o %以下、In : 5.094以下、Or :
18.0〜B0.0−1Ni : 1.0〜9.09&
、 MO: 0.6〜5.0 %、QuS 8.0 %
以下、N : 0.06〜0.80 %お工びP:0.
04%以下を、0.006〜0.10チのArと混入量
をo、ooaチ以下に抑制したSと共に含み、かつOa
を、S含有量に応じQa : (1〜lO)〔%S〕の
範囲において含有し、残部はFeおよび不可避不純物か
らなることを特徴とする、熱間加工性に優れた二相ステ
ンレス鋼である。This invention advantageously solves the above-mentioned problems, and even when using continuous casting materials that are prone to cracking, the occurrence of edge cracks is minimized, resulting in a significant improvement in yield.・With regard to the composition of duplex stainless steel, especially AI! This invention is based on new knowledge that it is extremely effective to limit S to a certain range, reduce S, and add Oa in accordance with this Si.0 Invention composition, that is, inventiveness, a: o, oa% or less, S to s
, o% or less, In: 5.094 or less, Or:
18.0~B0.0-1Ni: 1.0~9.09&
, MO: 0.6-5.0%, QuS 8.0%
Hereinafter, N: 0.06-0.80%, P: 0.
04% or less, together with 0.006 to 0.10 inches of Ar and S with the mixed amount suppressed to less than o, ooa degrees, and Oa
A duplex stainless steel with excellent hot workability, containing Qa: (1 to 1O) [%S] depending on the S content, with the remainder consisting of Fe and unavoidable impurities. be.
以下この発明を具体的に説明する0
まずこの発明において、成分組成を上記の範囲に限定し
た理由について述べる。This invention will be explained in detail below. First, the reason why the component composition is limited to the above range in this invention will be described.
0 : 0.08%以下
Cは、不可避的に鋼中に含まれる元素であるが0.08
%を超えて含有されると耐食性、耐粒界腐食性を劣化
させるので、上限を0,08チに定めた。0: 0.08% or less C is an element that is unavoidably contained in steel, but 0.08%
If the content exceeds 0.08%, the corrosion resistance and intergranular corrosion resistance will deteriorate, so the upper limit was set at 0.08%.
si : s、oチ以下
Siは、脱散剤として有用A元素であるが、含有量がg
、o係を超えるとσ相が発生して耐食性やじん性が著し
く劣化するので、上限を2.0%としたO
In : 6゜0%以下
罰は、強度を高める元素として、また相比率を調整する
元素として有用でおるが、含有量がbチを超えると耐食
性が劣化するので、上限は5.0係に定めた。si: s, o or less Si is an element A useful as a dispersing agent, but the content is
If the O coefficient exceeds , the σ phase will occur and the corrosion resistance and toughness will deteriorate significantly, so the upper limit was set at 2.0%.O In: 6°0% or less Although it is useful as an adjusting element, if the content exceeds B, the corrosion resistance deteriorates, so the upper limit was set at 5.0.
Or : 18.0〜80.0%
Qrは、耐食性の向上ならびにオーステナイト−フエラ
イ)S相組織の形成のためには不可欠の元素であって、
孔食や隙間腐食に対する抵抗性を考慮するとis、Oq
b未満ではその効果に乏しく、一方80.0%を超える
とσ相が析出し易くなってじん性が劣化する傾向にある
ので、Qr含有量は18.0〜80.0チの範囲に限定
し九〇’Ni : 1.0〜9.0 チ
Ni Vi、全面腐食に対する抵抗性の増加と2相組織
形成の面から不可欠な元素であるが、含有量が1.01
未満では十分な耐食性が得られず、一方9.0俤を超え
て含有されてもその改善効果は飽和に達するだけでなく
、高価でもあるので、1.0〜9.0チの範囲に限定し
九〇
Mo : 0.5〜6.096
MoVi、塩素イオンを含む腐食環境で生じる局部腐食
に対する抵抗性を同上させるのに有用な元素であるが、
含有量が0.5%に満たないとその添加効果に乏しく、
一方5.0%を超えて添加しても改善効果の増加は極め
て小さく、しかも高価な元素でもあるので、0.5〜5
.0チの範囲に限定したOcu : s、o%以下
Cuは、非酸化性酸に対する耐食性の改善に有効に寄与
するが、8.0%を超えて添加されると熱間加工性を劣
化させるので、上限を8.0%にしたON : 0.0
5〜0.80チ
Nけ、2相組織を形成するのに重要な元素であるほか、
耐食性の同上にも有効に寄与するが、0.059b未満
ではその添加効果に乏しく、一方0.80チを超えると
熱間加工性を著しく劣化させるので、含有量は0.0b
〜0.80係の範囲に限定したOP : 0.04係以
下
Pは、不可避に混入する不純物であって、熱間加工性の
改善に有害な元素であるが、0.04%tでなら許容で
きる◎
AI!: 0.005〜O,lO%
AI!は、この発明鋼種の熱間加工性を劣化させる酸素
を減少させるのに有用な元素であるが、0.005チ未
満ではその添加効果に乏しく、熱間加工性を改善して満
足のいく程度に圧延時における割れの発生を抑制するた
めには、0.0064以上を含有させる必要がある・
第1図に、鋼中hp量が熱間加工性に及は1影響につい
て調べた結果を示す。実験は、C:約0.02%、Si
: 1 %以下、Mn : 0.5 % 〜1 %、
Or : 22.0〜28.0 %、Ni : 5.0
〜7.0%、M。Or: 18.0-80.0% Qr is an essential element for improving corrosion resistance and forming an austenite-ferrite S phase structure,
Considering resistance to pitting corrosion and crevice corrosion, is, Oq
If it is less than b, the effect is poor, while if it exceeds 80.0%, the σ phase tends to precipitate and the toughness tends to deteriorate, so the Qr content is limited to a range of 18.0 to 80.0 h. Ni: 1.0 to 9.0 Ni Vi is an essential element from the viewpoint of increasing resistance to general corrosion and forming a two-phase structure, but the content is 1.01
If the content is less than 9.0 tres, sufficient corrosion resistance cannot be obtained, while if the content exceeds 9.0 tres, the improvement effect not only reaches saturation but is also expensive, so it is limited to the range of 1.0 to 9.0 tres. Mo: 0.5 to 6.096 MoVi is an element useful for increasing resistance to local corrosion that occurs in a corrosive environment containing chlorine ions, but
If the content is less than 0.5%, the addition effect will be poor,
On the other hand, even if it is added in an amount exceeding 5.0%, the improvement effect will be extremely small, and since it is an expensive element,
.. Ocu limited to the range of 0%: s,o% Cu effectively contributes to improving corrosion resistance against non-oxidizing acids, but when added in excess of 8.0%, it deteriorates hot workability. Therefore, ON with the upper limit set to 8.0%: 0.0
In addition to being an important element for forming a two-phase structure,
Although it effectively contributes to corrosion resistance, if it is less than 0.059b, its addition effect is poor, while if it exceeds 0.80b, hot workability will be significantly deteriorated, so the content should be 0.0b.
OP limited to the range of ~0.80 modulus: 0.04 modulus or less P is an impurity that is inevitably mixed in and is an element harmful to improving hot workability, but at 0.04% t. Acceptable◎ AI! : 0.005~O,lO% AI! is an element useful for reducing oxygen, which deteriorates the hot workability of the steel of the present invention, but if it is less than 0.005%, the effect of its addition is poor, and the hot workability cannot be improved to a satisfactory degree. In order to suppress the occurrence of cracks during rolling, it is necessary to contain 0.0064 or more. Figure 1 shows the results of investigating the effect of HP in steel on hot workability. . In the experiment, C: about 0.02%, Si
: 1% or less, Mn: 0.5% to 1%,
Or: 22.0-28.0%, Ni: 5.0
~7.0%, M.
: 1.0〜4.0%、Cu : 8 %以下、N :
(1,10〜0.20チ、P : 0.002〜0.
04 チ、S : 0.0005〜0.008係、そし
てOa/S比が8〜5の組成になり、960℃でのフェ
ライト量が80〜60チの試料について、950℃にお
ける高温、高速引張り試験を行ない、その断面減少率に
ついて調べた0耳割れの発生しない断面減少率の限界は
70%であるが、AI!量が0.005%に満たないと
その限界断面率を下まわっている。: 1.0 to 4.0%, Cu: 8% or less, N:
(1,10~0.20chi, P: 0.002~0.
04 Chi, S: 0.0005 to 0.008, and a composition with an Oa/S ratio of 8 to 5, and a sample with a ferrite amount of 80 to 60 at 960°C, was subjected to high-temperature, high-speed tensile testing at 950°C. A test was conducted to find out the cross-sectional reduction rate.The limit of the cross-sectional reduction rate at which zero-edge cracking does not occur is 70%, but AI! If the amount is less than 0.005%, it is below the critical section ratio.
とはいえAI!量が0.10%を超えると、アルミナク
ラスターによる表面欠陥が増大するので、A/含有量は
0.005〜0.10%の範囲に限定したO3 : o
、ooa%以下
Sは、鋼中に不可避に混入する不純物であって、とりわ
けこの発明に係る鋼徨の熱間加工性にとっては有害な元
素であり、その含有量が0.008%を超えると、後述
するCaを添加しても硫化物の量が増大してCaの添加
による効果が減殺されるだけでなく、溶接性も悪化する
ので、S含有量は0.008%以下の範囲に抑制するこ
ととした。However, AI! If the amount exceeds 0.10%, surface defects due to alumina clusters will increase, so the A/O content is limited to a range of 0.005 to 0.10%.
, ooa% or less S is an impurity that inevitably mixes into steel, and is an element that is particularly harmful to the hot workability of the steel according to the present invention, and if its content exceeds 0.008%. Even if Ca, which will be described later, is added, the amount of sulfide increases, which not only reduces the effect of Ca addition, but also deteriorates weldability, so the S content is suppressed to a range of 0.008% or less. It was decided to.
Ca : (1〜10)(%5)
Caは、強力な硫化物形成元素であり、硫化物を形成す
ることによって固溶Sを低減させ、熱間加工性の改善に
有効に寄与する。しかしながら、ただ単に添加したとし
ても、添加量が固溶Sの固定に必要とする量に満たない
場合にはその添加効果に乏しく、一方固溶S量に較べて
添加量が多すぎると溶接性が悪化する0従ってQaは、
S量との兼合いで適切量を添加することが肝要なわけで
あるO
第2因に、0 : 0.02%、Si : 0.4 ’
Iy、Mn:1.5 %、Or:zs4、Ni : 5
.5 %、M□ : 89bsN : 0.15チ、P
≦0.04チ、AI!≧Q、005%そしてS≦0.0
08チを基本成分とする鋼に、Caを種種の範囲で添加
し几場合の熱間加工性について調べた結果を、0シ、比
と高温高速引張り試験におゆる断面減少率との関係で示
す。Ca: (1 to 10) (%5) Ca is a strong sulfide-forming element, reduces solid solution S by forming sulfides, and effectively contributes to improving hot workability. However, even if it is simply added, if the amount added is less than the amount required to fix solid solution S, the addition effect will be poor, and on the other hand, if the amount added is too large compared to the amount of solid solution S, weldability will deteriorate. becomes worse 0 Therefore, Qa is
It is important to add an appropriate amount in balance with the amount of S.The second factor is 0: 0.02%, Si: 0.4'
Iy, Mn: 1.5%, Or: zs4, Ni: 5
.. 5%, M□: 89bsN: 0.15ch, P
≦0.04chi, AI! ≧Q, 005% and S≦0.0
The results of an investigation of the hot workability of a steel whose basic component is 0.08% Ca and 0.08% Ca were added in various types were compared with the relationship between the 0% ratio and the cross-section reduction rate in a high-temperature, high-speed tensile test. show.
同図よシ明らかなように、Ca/8が1に満たないと断
面減少率が70%を下まわるので0a/sの下限は1に
定めた〇一方0a/sが10を超えると、Oaの添加効
果が飽和に達するだけでなく、酸化物や硫化物による表
面欠陥が発生するおそれが大金<、まfcCaの添加量
が多くなると上述したように溶接性も阻害されるので、
。a/sの上限はlOに定めた◎
実 施 例
表1に示した成分組成になる各徨溶鋼(供試材41〜I
EI)を連続鋳造法によって、S OOrnm厚のスラ
ブとしたのち、18(lsmHまで分塊圧延し、ついで
再加熱してから4闘]で熱間圧延を施した0
得られた熱延板における耳割れの発生状況について調べ
た結果を、表1に併記する0なお幅方向における耳割れ
の長さがl Q mm未満の場合には、実害は小さく、
合格品として許容できるものでろるO
A/含有量がこの発明の適正範囲を下回る供試材A1お
よび8、またCa量が適正量に満たない同4Bおよび6
、さらにN量およびS量が上限を超えて含まれる同ム4
お工び5ではいずれも、20 mm以上の耳割れが発生
した〇
これに対しこの発明の適正範囲を満足する実施例(供試
材/467〜18)はいずれも、耳割れの発生程度は極
めて小感<、最大のものでも高々111mmにすぎなか
った。As is clear from the figure, when Ca/8 is less than 1, the area reduction rate is less than 70%, so the lower limit of 0a/s is set to 1.On the other hand, when 0a/s exceeds 10, Not only does the effect of adding Oa reach saturation, but also there is a risk that surface defects due to oxides and sulfides will occur, and if the amount of Ca added increases, weldability will also be inhibited as described above.
. The upper limit of a/s was set at lO.
EI) was made into a slab with a thickness of SOOrnm by a continuous casting method, and then hot rolled at 18 (blush rolling to lsmH, then reheated and then 4 cycles). The results of investigating the occurrence of ear cracks are shown in Table 1.0 If the length of the ear crack in the width direction is less than l Q mm, the actual damage will be small;
Test materials A1 and 8 whose O A/content is below the appropriate range of this invention, and test materials 4B and 6 whose Ca content is below the appropriate range, are acceptable as acceptable products.
, and further contains the amount of N and S exceeding the upper limit 4
In all cases of Machining 5, edge cracks of 20 mm or more occurred.On the other hand, in all of the examples (sample materials/467 to 18) that satisfied the appropriate range of this invention, the degree of edge cracks occurred. It felt extremely small, and the largest one was only 111 mm at most.
発明の効果
かくしてこの発明によれば、オーステナイト−7エライ
トニ相ステンレス鋼において従来懸念された熱間加工に
おける割れの発生を大幅に低減することができ、従って
歩留りの向上も併せて実現できる。Effects of the Invention Thus, according to the present invention, it is possible to significantly reduce the occurrence of cracking during hot working, which was a concern in the past in austenitic-7elite dual-phase stainless steel, and therefore, it is also possible to improve the yield.
wJ1図は、鋼中Ajが熱間加工性に及ばず影響をAl
量と断面減少率との関係で示したグラフ、第2図は、同
じく0a/sと断面減少率との関係を・示したグラフで
ある0
特許出願人 川崎製鉄株式会社
第1図
Al量(壷量%)
断面減少、!!(匍Figure wJ1 shows that Aj in steel does not affect hot workability and Al
Figure 2 is a graph showing the relationship between 0a/s and area reduction rate.0 Patent applicant: Kawasaki Steel Corporation Figure 1 Al amount ( Urn volume %) cross section reduction,! ! (crawl
Claims (1)
0〜9.0重量係、 MO: 0.5〜5.0重量−1 Ou : 13.0重量%以下、 N : 0.05〜0.80重量%およびP:0.04
重量%以下 を、 0.005〜0.10重量%のAlと混入量をo、oo
s・重量%以下に抑制したSと共に含み、かつQaを、
S含有量に応じ、 (3a : (1〜10)(SS) の範囲において含有し、残部はF8および不可避不純物
からなることを特徴とする・熱間加工性に優れた二相ス
テンレス鋼。[Claims] LG: 0.08% by weight or less, Si: 2.0% by weight or less, Mn: 5.0% by weight or less, Or: 18.0-8o, O weight ratio, Ni: 1.
0 to 9.0 weight ratio, MO: 0.5 to 5.0 weight-1 Ou: 13.0 weight% or less, N: 0.05 to 0.80 weight%, and P: 0.04
% by weight or less, 0.005 to 0.10% by weight of Al and mixing amount o, oo
Contains S with S suppressed to s·wt% or less, and Qa,
A duplex stainless steel with excellent hot workability, characterized in that the S content is in the range of (3a: (1 to 10) (SS), with the remainder consisting of F8 and inevitable impurities.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP11955084A JPS60262946A (en) | 1984-06-11 | 1984-06-11 | Two-phase stainless steel with superior hot workability |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP11955084A JPS60262946A (en) | 1984-06-11 | 1984-06-11 | Two-phase stainless steel with superior hot workability |
Publications (2)
Publication Number | Publication Date |
---|---|
JPS60262946A true JPS60262946A (en) | 1985-12-26 |
JPH0119465B2 JPH0119465B2 (en) | 1989-04-11 |
Family
ID=14764082
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP11955084A Granted JPS60262946A (en) | 1984-06-11 | 1984-06-11 | Two-phase stainless steel with superior hot workability |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPS60262946A (en) |
Cited By (10)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6289848A (en) * | 1985-08-26 | 1987-04-24 | Nippon Stainless Steel Co Ltd | Two-phase stainless steel for rolling stock having high strength and high corrosion resistance and excellent in young's modulus and hot workability |
JPS62202021A (en) * | 1986-02-28 | 1987-09-05 | Nippon Chiyuutankou Kk | Manufacture of cast steel product excellent in weldability and resistance to environmental corrosion |
US4721600A (en) * | 1985-03-28 | 1988-01-26 | Sumitomo Metal Industries, Ltd. | Superplastic ferrous duplex-phase alloy and a hot working method therefor |
JPS63157838A (en) * | 1986-12-18 | 1988-06-30 | Kawasaki Steel Corp | Two-phase stainless steel excellent in crevice corrosion resistance |
JPH01225754A (en) * | 1988-02-04 | 1989-09-08 | Armco Advanced Materials Corp | Double molten high manganese stainless steel |
JPH02258956A (en) * | 1989-03-29 | 1990-10-19 | Sumitomo Metal Ind Ltd | Highly corrosion resistant duplex phase stainless steel excellent in hot workability |
JPH0741907A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
JPH0741906A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
JP2012510491A (en) * | 2008-12-01 | 2012-05-10 | ロディア オペレーションズ | Method for producing adipic acid |
JP2020059900A (en) * | 2018-10-12 | 2020-04-16 | 日鉄ステンレス株式会社 | Resource-saving two-phase stainless steel excellent in corrosion resistance |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS58224155A (en) * | 1982-06-19 | 1983-12-26 | Kawasaki Steel Corp | Seamless two-phase stainless steel pipe and its manufacture |
-
1984
- 1984-06-11 JP JP11955084A patent/JPS60262946A/en active Granted
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS58224155A (en) * | 1982-06-19 | 1983-12-26 | Kawasaki Steel Corp | Seamless two-phase stainless steel pipe and its manufacture |
Cited By (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US4721600A (en) * | 1985-03-28 | 1988-01-26 | Sumitomo Metal Industries, Ltd. | Superplastic ferrous duplex-phase alloy and a hot working method therefor |
JPS6289848A (en) * | 1985-08-26 | 1987-04-24 | Nippon Stainless Steel Co Ltd | Two-phase stainless steel for rolling stock having high strength and high corrosion resistance and excellent in young's modulus and hot workability |
JPH0239583B2 (en) * | 1985-08-26 | 1990-09-06 | Nippon Stainless Steel Co | |
JPS62202021A (en) * | 1986-02-28 | 1987-09-05 | Nippon Chiyuutankou Kk | Manufacture of cast steel product excellent in weldability and resistance to environmental corrosion |
JPS63157838A (en) * | 1986-12-18 | 1988-06-30 | Kawasaki Steel Corp | Two-phase stainless steel excellent in crevice corrosion resistance |
JPH01225754A (en) * | 1988-02-04 | 1989-09-08 | Armco Advanced Materials Corp | Double molten high manganese stainless steel |
JPH02258956A (en) * | 1989-03-29 | 1990-10-19 | Sumitomo Metal Ind Ltd | Highly corrosion resistant duplex phase stainless steel excellent in hot workability |
JPH0717987B2 (en) * | 1989-03-29 | 1995-03-01 | 住友金属工業株式会社 | Highly corrosion resistant duplex stainless steel with excellent hot workability |
JPH0741907A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
JPH0741906A (en) * | 1993-07-28 | 1995-02-10 | Nippon Yakin Kogyo Co Ltd | Superplastic two-phase stainless steel |
JP2012510491A (en) * | 2008-12-01 | 2012-05-10 | ロディア オペレーションズ | Method for producing adipic acid |
JP2020059900A (en) * | 2018-10-12 | 2020-04-16 | 日鉄ステンレス株式会社 | Resource-saving two-phase stainless steel excellent in corrosion resistance |
Also Published As
Publication number | Publication date |
---|---|
JPH0119465B2 (en) | 1989-04-11 |
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