JPH0768603B2 - Duplex stainless steel for building materials - Google Patents
Duplex stainless steel for building materialsInfo
- Publication number
- JPH0768603B2 JPH0768603B2 JP1126665A JP12666589A JPH0768603B2 JP H0768603 B2 JPH0768603 B2 JP H0768603B2 JP 1126665 A JP1126665 A JP 1126665A JP 12666589 A JP12666589 A JP 12666589A JP H0768603 B2 JPH0768603 B2 JP H0768603B2
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- Prior art keywords
- stainless steel
- steel
- less
- duplex stainless
- building materials
- Prior art date
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Description
【発明の詳細な説明】 （産業上の利用分野） 本発明は建築建材用として使用される強度が高くレラク
セーション（ステンレス鋼にある応力を与え、その時に
生ずる歪が一定に保たれるような条件で放置すると、時
間の経過とともに初めに与える応力が次第に減少する現
象で、その減少の小さい程すぐれた性質と評価されてい
る。）の小さい安価なオーステナイト・フェライト系二
相ステンレス鋼に関する。DETAILED DESCRIPTION OF THE INVENTION (Industrial field of application) The present invention is used as a building material for high strength and relaxation (provides a certain stress to stainless steel so that the strain generated at that time is kept constant). It is a phenomenon in which the stress initially applied is gradually reduced with the passage of time under various conditions, and it is evaluated that the smaller the decrease, the better the properties.) And the less expensive austenitic-ferritic duplex stainless steel.
（従来の技術） 従来建築建材用には安価で強度が高い理由で、例えばJI
Sに規定されたSM鋼のような普通炭素鋼が使用されてき
たが、普通炭素鋼は耐食性をもたないために無塗装で使
用される場合はもちろん、たとえ塗装して使用される場
合でも腐食による消耗は避けられず建築構造物としての
寿命が短くなる原因になり、また発錆により美観も損な
われるなどの欠点をもっている。このような現状におい
て、将来は耐久性や美観の点でこれらの普通炭素鋼にか
わりステンレス鋼の使用が期待されている。しかしなが
ら、従来のステンレス鋼をこのような用途に使用する場
合幾つかの問題がある。たとえば、SUS304やSUS316など
に代表されるオーステナイト系ステンレス鋼は、溶接性
が優れているためステンレス鋼の中でも最も適している
ように思われるが、一般に強度（耐力）がやゝ低いため
レラクセーションが大きい。その上、多量のNiを含有す
るために高価である。また、SUS410で代表されるマルテ
ンサイト系ステンレス鋼やSUS430に代表されるフェライ
ト系ステンレス鋼はレラクセーションも小さく、オース
テナイト系ステンレス鋼に比べれば安価であるが、溶接
性が劣る問題点がある。またこれらのオーステナイト系
と、マルテンサイト系やフェライト系ステンレス鋼の中
間的な特性をもつ鋼としてSUS329J1に代表されるオース
テナイト・フェライト二相ステンレス鋼があるが、この
鋼はオーステナイト系と同等程度に溶接性が優れ、オー
ステナイト系ステンレス鋼の欠点である粒界腐食や応力
腐食割れに対する抵抗性も強いことから化学機器などに
多く使用されている。(Prior art) For the reason that it is inexpensive and has high strength for conventional building materials, for example, JI
Although ordinary carbon steel such as SM steel specified in S has been used, ordinary carbon steel has no corrosion resistance and is therefore used not only when it is unpainted but also when it is used by painting. It is inevitable to wear out due to corrosion, which causes the life of the building structure to be shortened, and it has drawbacks such as aesthetic deterioration due to rusting. Under these circumstances, it is expected that stainless steel will be used in place of these ordinary carbon steels in terms of durability and aesthetics in the future. However, there are some problems with using conventional stainless steel for such applications. For example, austenitic stainless steels such as SUS304 and SUS316 are considered to be the most suitable among the stainless steels because of their excellent weldability, but they are generally weaker in strength (proof stress), so relaxation Is big. In addition, it is expensive because it contains a large amount of Ni. Further, the martensitic stainless steel typified by SUS410 and the ferritic stainless steel typified by SUS430 have small relaxation and are less expensive than austenitic stainless steel, but have a problem of poor weldability. In addition, there is austenite-ferrite duplex stainless steel represented by SUS329J1 as a steel that has intermediate properties between these austenitic and martensitic or ferritic stainless steels, but this steel is welded to the same extent as austenitic stainless steels. It is widely used in chemical equipment because of its excellent properties and strong resistance to intergranular corrosion and stress corrosion cracking, which are the drawbacks of austenitic stainless steel.
（発明が解決しようとする課題） 本発明は上述したような溶接性に優れた二相ステンレス
鋼に着目し、その成分を特定することによってレラクセ
ーションが著しく小さく且つ建築建材用に一般的に要求
されるJIS SM 41,50と同等あるいはそれ以上の機械的性
質すなわち、室温での耐力（PS）が40kgf/mm2以上、引
張り強さ（TS）が60kgf/mm2以上、伸び（El）が20％以
上、０℃におけるシャルピー吸収エネルギー（vEo）が
2.8kg・ｍ以上であって、室温におけるレラクセーショ
ンが小さいという特性を有する建築建材用二相ステンレ
ス鋼を提供することを目的とするものである。(Problems to be Solved by the Invention) The present invention focuses on duplex stainless steel having excellent weldability as described above, and by specifying its components, relaxation is extremely small and generally used for building materials. equivalent required JIS SM 41 and 50 or more mechanical properties i.e., yield strength at room temperature (PS) is 40 kgf / mm 2 or more, tensile strength (TS) is 60 kgf / mm 2 or more, elongation (El) Is 20% or more, and the Charpy absorbed energy (vEo) at 0 ° C is
It is an object of the present invention to provide a duplex stainless steel for building materials having a property of 2.8 kg · m or more and having low relaxation at room temperature.
（課題を解決するための手段） 本発明は、 （１） C:0.10％以下、Si:0.1〜3.0％、Mn:0.1〜4.0％
未満、Cr:19.0〜26.0％、Ni:1.0〜6.0％、N:0.05〜0.40
％を含有し、残りが鉄および不可避的不純物から成り、
かつオーステナイト相面積率が20〜80％であることを特
徴とする建築建材用二相ステンレス鋼、 （２） C:0.10％以下、Si:0.1〜3.0％、Mn:0.1〜4.0％
未満、Cr:19.0〜26.0％、Ni:1.0〜6.0％、N:0.05〜0.40
％、およびNb:0.01〜2.0％、Ti:0.01〜2.0％、V:0.01〜
2.0％のうち１種あるいは２種以上を含有し、残りが鉄
および不可避的不純物から成り、かつオーステナイト相
面積率が20〜80％であることを特徴とする建築建材用二
相ステンレス鋼、 である。(Means for Solving the Problems) The present invention provides (1) C: 0.10% or less, Si: 0.1 to 3.0%, Mn: 0.1 to 4.0%
Less than, Cr: 19.0 to 26.0%, Ni: 1.0 to 6.0%, N: 0.05 to 0.40
%, The balance consisting of iron and unavoidable impurities,
And the austenite phase area ratio is 20-80%, duplex stainless steel for building construction materials, (2) C: 0.10% or less, Si: 0.1-3.0%, Mn: 0.1-4.0%
Less than, Cr: 19.0 to 26.0%, Ni: 1.0 to 6.0%, N: 0.05 to 0.40
%, Nb: 0.01 to 2.0%, Ti: 0.01 to 2.0%, V: 0.01 to
2. Duplex stainless steel for building materials, containing one or more of 2.0%, the rest consisting of iron and unavoidable impurities, and having an austenite phase area ratio of 20 to 80%. is there.
以下に、本発明鋼について詳細に説明する。The steel of the present invention will be described in detail below.
SUS329J1で代表される現行二相ステンレス鋼は孔食や応
力腐食割れに対する抵抗性を高めるために高価な合金成
分のMoを通常数％含有している。しかし、建築材料とし
て使用される場合には、Cl-環境は少いので孔食や応力
腐食割れに起因する損傷が起こることは少なく、必然的
に適正な鋼成分も変わってくる。このような前提のもと
に、各種機械的性質に与える二相ステンレス鋼の相バラ
ンス支配元素としてCr,Ni,Mn,N,Siなど、および強化元
素としてNb,Ti,Vなどの各種元素の影響を調べた結果、
C:0.10％以下、Si:0.1〜3.0％、Mn:0.1〜4.0％未満、C
r:19.0〜26.0％、Ni:1.0〜6.0％、N:0.05〜0.40％を含
有しあるいはさらにNb:0.01〜2.0％、Ti:0.01〜2.0％、
V:0.01〜2.0％の１種または２種以上を含む鋼により目
標の特性を満足できることがわかった。Current duplex stainless steels represented by SUS329J1 usually contain several percent of expensive alloying component Mo to enhance resistance to pitting and stress corrosion cracking. However, when used as a building material, since the Cl - environment is small, damage due to pitting and stress corrosion cracking is unlikely to occur, and the proper steel composition also inevitably changes. Based on these assumptions, Cr, Ni, Mn, N, Si, etc. as the phase balance controlling elements of the duplex stainless steel given to various mechanical properties, and Nb, Ti, V etc. as the strengthening elements As a result of examining the influence,
C: 0.10% or less, Si: 0.1 to 3.0%, Mn: 0.1 to less than 4.0%, C
r: 19.0 to 26.0%, Ni: 1.0 to 6.0%, N: 0.05 to 0.40% or Nb: 0.01 to 2.0%, Ti: 0.01 to 2.0%,
It was found that the target properties can be satisfied by steel containing one or more of V: 0.01 to 2.0%.
このように鋼成分を限定した理由は次のとおりである。The reasons for limiting the steel components in this way are as follows.
C:Crを多量に含むステンレス鋼においてＣの含有はクロ
ム炭化物を生成して粒界に析出し、耐食性を低下させる
ため、その含有量を0.15％以下にした。In stainless steel containing a large amount of C: Cr, the content of C forms 0.15% or less because it forms chromium carbides and precipitates at grain boundaries, which lowers the corrosion resistance.
Si:フェライト形成元素で二相鋼におけるフェライト相
の量をコントロールする。そしてこの元素の添加により
有効に強度を上げることができる。この強化のためには
少なくとも0.1％添加しなければその効果を発揮するこ
とができず、この含有量の増加に強度を増大せしめるが
過剰の添加は熱間加工性を低下させるため３％以下とす
る必要がある。Si: Ferrite forming element that controls the amount of ferrite phase in duplex stainless steel. The strength can be effectively increased by adding this element. In order to strengthen this, the effect cannot be exhibited unless it is added at least 0.1%, and increasing the content increases the strength, but excessive addition reduces the hot workability, so it is 3% or less. There is a need to.
Mn:Niのかわりに使用する安価で有力なオーステナイト
形成元素で、二相鋼におけるオーステナイト相の量をコ
ントロールし、レラクセーションを安定して小さくする
作用する役目をもつ。そしてこの成分の添加により有効
に強度を増大する。この強化のためには少なくとも0.1
％添加しなければその効果を発揮することができない。
また、Mnの過剰添加はオーステナイト相を増やしレラク
セーションを高めるため、４％未満でなければならな
い。It is an inexpensive and powerful austenite-forming element used in place of Mn: Ni, and has the role of controlling the amount of austenite phase in duplex stainless steel and stabilizing and reducing relaxation. The addition of this component effectively increases the strength. At least 0.1 for this enhancement
If it is not added, the effect cannot be exhibited.
Further, the excessive addition of Mn increases the austenite phase and enhances relaxation, so it must be less than 4%.
Cr:耐食性保有のためと、フェライト形成元素であるた
めフェライト相の量のコントロールのために必要な元素
で、そのためには少なくとも19.0％以上含有しなければ
ならない。しかし、いたずらに多量の含有は合金コスト
が高くなるだけである。したがって、その上限を26％に
した。Cr: This element is necessary for maintaining corrosion resistance and for controlling the amount of ferrite phase because it is a ferrite-forming element. For that purpose, at least 19.0% or more must be contained. However, an unnecessarily large content only increases the alloy cost. Therefore, the upper limit was set to 26%.
Ni:二相鋼におけるオーステナイト相形成に必要な元素
で、そのためには少なくとも１％含有しなければならな
い。しかし多量の添加は相バランスとしてオーステナイ
ト相の割合を増やし、レラクセーションを高め、その上
合金コストが高くなるのでその量は６％以下でなければ
ならない。Ni: An element necessary for forming an austenite phase in a duplex stainless steel, and for this purpose, it must be contained at least 1%. However, the addition of a large amount increases the proportion of the austenite phase as a phase balance, increases the relaxation, and increases the alloy cost, so the amount must be 6% or less.
N:Niと同じように二相鋼においてオーステナイト相を増
やし強度を上げる元素で、そのためには少なくとも0.05
％含有しなければならない。しかし多量の添加は相バラ
ンスとしてオーステナイト相の割合を増やし、さらに気
泡発生による内部欠陥生成の原因になるため、0.40％以
下でなければならない。Like N: Ni, it is an element that increases the austenite phase and increases the strength in duplex stainless steels.
% Must be included. However, addition of a large amount increases the proportion of the austenite phase as a phase balance, and further causes the generation of internal defects due to the generation of bubbles, so it must be 0.40% or less.
これらの合金元素の他に、強化元素として、Nb:0.01〜
2.0％、Ti:0.01〜2.0％、およびV:0.01〜2.0％のうち１
種または２種以上を含有させることができる。すなわ
ち、これらの元素を0.01％以上含有することにより結晶
粒が微細になり強度とくに降伏強度を上昇せしめる。し
かし多量の添加は靱性を著しく低下せしめる結果となる
ため、2.0％以下でなければならない。In addition to these alloying elements, Nb: 0.01-
2.0%, Ti: 0.01 to 2.0%, and V: 0.01 to 2.0%, 1
One kind or two or more kinds can be contained. That is, by containing 0.01% or more of these elements, the crystal grains become fine and the strength, particularly the yield strength, is increased. However, addition of a large amount results in a significant decrease in toughness, so it must be 2.0% or less.
また、本発明鋼は、このような合金成分範囲を満足する
と同時に、製品として、必ずオーステナイト相とフェラ
イト相との二相から成らなければならず、それの存在比
率は面積百分率で20〜80％好ましくは30〜70％である。
第１図に本発明鋼すなわち建築建材用鋼の特性の一つと
して要求されるレラクセーションと、オーステナイト相
面積百分率（％）との関係を示したが、これによりオー
ステナイト相が80％を超えるとレラクセーションが急激
に大きくなることがわかる。また20％を切ると、後述す
る実施例からもわかるように目標とする機械的性質が得
られない。本発明はこのような比率を満足することによ
って、建築建材用として必要な諸性質を一層改善する。Further, the steel of the present invention, while satisfying such an alloy component range, as a product, must necessarily consist of two phases of an austenite phase and a ferrite phase, and the abundance ratio thereof is 20 to 80% in area percentage. It is preferably 30 to 70%.
Fig. 1 shows the relationship between the relaxation required as one of the properties of the steel of the present invention, that is, the steel for building materials, and the austenite phase area percentage (%). As a result, the austenite phase exceeds 80%. It can be seen that relaxation increases rapidly. If it is less than 20%, the desired mechanical properties cannot be obtained, as will be understood from the examples described later. By satisfying such a ratio, the present invention further improves various properties required for building materials.
以下に実施例により説明する。An example will be described below.
実施例 １ C:0.01〜0.03％、Si:0.4〜0.7％、Mn:1.7〜1.8％、Cr:1
7.0〜23.0％、Ni:6％以下、Mo:3％以下、N:0.12〜0.17
％を含む20kgの鋼塊を真空誘導溶解炉により溶製し、こ
れらの鋼塊を厚さ13mmに熱間圧延した後、1100℃で30分
間保定したのち水焼入れよりなる溶体化処理を行い、材
質調査を行った。Cr及びNiの含有量とγ相の面積百分
率、PS,TS,El,vEoの値との関係を第２図（Ａ）〜（Ｅ）
に示す。この結果から、Cr量が19％に満たない場合には
γ相面積百分率は20％に満たずまたα′マルテンサイト
が生成してPSやTSが著しく高くElは20％に満たない。す
なわち、本発明の目標特性を満足するためにはCrは19.0
％以上でなければならない。Niについては、１％に満た
ない場合にはα相だけより成り、したがってvEoは極め
て低い。６％を超えた場合にはγ相が多くなり、レラク
セーションを小さくできない。このような理由から、Ni
量は1.0〜6.0％の範囲でなければならない。Example 1 C: 0.01 to 0.03%, Si: 0.4 to 0.7%, Mn: 1.7 to 1.8%, Cr: 1
7.0-23.0%, Ni: 6% or less, Mo: 3% or less, N: 0.12-0.17
% Ingot in a vacuum induction melting furnace, hot-roll these steel ingots to a thickness of 13 mm, hold them at 1100 ° C. for 30 minutes, then perform solution treatment by water quenching, Material survey was conducted. The relationship between the Cr and Ni contents and the area percentage of the γ phase and the values of PS, TS, El and vEo are shown in FIGS.
Shown in. From this result, when the Cr content is less than 19%, the γ phase area percentage is less than 20%, and α ′ martensite is formed, PS and TS are remarkably high, and El is less than 20%. That is, in order to satisfy the target characteristics of the present invention, Cr is 19.0
Must be at least%. For Ni, less than 1% consists only of the α phase and therefore vEo is very low. If it exceeds 6%, the γ phase increases and the relaxation cannot be reduced. For this reason, Ni
The amount should be in the range of 1.0-6.0%.
実施例 ２ 真空誘導溶解炉により、C:0.01〜0.08％、Si:0.5〜2.7
％、Mn:0.8〜3.9％、Ni:1.9〜4.5％、Cr:19〜26％、N:
0.09〜0.32％、その他に選択元素として、Nb:0.05〜0.1
2％、Ti:0.10〜0.20％およびV:0.05〜0.10％を含む第１
表に示すような組成の鋼塊を作製した。これらの鋼塊を
厚さ25mmに熱間圧延した後、1050〜1150℃で溶体化熱処
理を行った。これらの鋼板の引張特性値、衝撃特性値お
よびレラクセーション率を第２表に示した。レラクセー
ション率は初期応力＝耐力×0.8、試験温度＝20℃±0.5
℃、試験時間＝10hrにて、自動制御槓桿型レラクセーシ
ョン試験機により、JIS Z 2276に準拠して測定した。Example 2 C: 0.01-0.08%, Si: 0.5-2.7 by a vacuum induction melting furnace
%, Mn: 0.8 to 3.9%, Ni: 1.9 to 4.5%, Cr: 19 to 26%, N:
0.09-0.32%, and Nb: 0.05-0.1 as other selective elements
1% including 2%, Ti: 0.10-0.20% and V: 0.05-0.10%
Steel ingots having the compositions shown in the table were produced. After hot rolling these steel ingots to a thickness of 25 mm, solution heat treatment was performed at 1050-1150 ° C. Table 2 shows the tensile property value, impact property value and relaxation rate of these steel sheets. The relaxation rate is initial stress = proof stress x 0.8, test temperature = 20 ° C ± 0.5
It was measured in accordance with JIS Z 2276 by an automatic control ladle type relaxation tester at a temperature of ℃ for 10 hours.
第１表および第２表において、鋼No.1〜15の鋼は本発明
鋼であるが、No.16はSUS304、No.17はSUS410、No.18はS
M40の代表例を比較鋼として示している。In Tables 1 and 2, steel Nos. 1 to 15 are steels of the present invention, but No. 16 is SUS304, No. 17 is SUS410, and No. 18 is S.
A representative example of M40 is shown as a comparative steel.
No.1〜15の本発明鋼はオーステナイト相とフェライト相
より成る二相組織でそれらのオーステナイト相の占める
面積百分率は30〜70％の範囲に入っていた。これらの本
発明鋼の機械的性質は目標とするPS40kgf/mm2以上、TS6
0kgf/mm2以上、El20％以上、vEo2.8kgf・ｍ以上を十分
に満足し、特にPSとTSの強度は比較鋼のSUS304,SUS410
およびSM40よりはるかに高い。また本発明鋼の常温にお
けるレラクセーションはSM鋼に近くきわめて小さく建築
構造物用として適している。The steels of the present invention Nos. 1 to 15 had a two-phase structure composed of an austenite phase and a ferrite phase, and the area percentage occupied by these austenite phases was in the range of 30 to 70%. The mechanical properties of these steels of the present invention are PS40kgf / mm 2 or more, TS6
Sufficiently satisfying 0kgf / mm 2 or more, El 20% or more, vEo 2.8kgf ・ m or more, especially the strength of PS and TS is SUS304, SUS410 of comparative steel
And much higher than the SM40. Further, the relaxation of the steel of the present invention at room temperature is very close to that of SM steel and is suitable for building structures.
なお、本発明鋼は、ステンレス鋼の溶製法としてよく知
られた、転炉や電気炉と真空脱炭精錬などとの組合せで
溶製され、連続鋳造、または造塊と分塊圧延によりスラ
ブにされる。このスラブは一旦室温にまで冷却されるか
あるいは必ずしも室温にまで冷却されることなく加熱炉
に装入して加熱した後1200〜600℃の温度範囲で厚板に
圧延される。圧延後の冷却は自然放冷でもよいし水冷な
どの強制冷却でもよい。続いて必要に応じ950〜1200℃
の温度範囲で溶体化熱処理が行われる。The steel of the present invention is well-known as a melting method for stainless steel, is melted by a combination of a converter or an electric furnace and vacuum decarburization refining, and is continuously cast, or formed into a slab by ingot casting and slabbing. To be done. This slab is once cooled to room temperature, or is not necessarily cooled to room temperature but is charged into a heating furnace and heated, and then rolled into a thick plate in a temperature range of 1200 to 600 ° C. Cooling after rolling may be natural cooling or forced cooling such as water cooling. Then 950-1200 ℃ if necessary
Solution heat treatment is performed in the temperature range of.
（発明の効果） 以上説明したように、本発明は成分を特定することによ
り、SM41,50クラスと同等或はそれ以上の特性をもち、
しかもレラクセーションが小さいことから建築建材用に
適した二相ステンレス鋼を安価に製造できるので、工業
的価値は極めて大きい。 (Effects of the Invention) As described above, the present invention has characteristics equal to or higher than the SM41,50 class by specifying the components,
Moreover, since the relaxation is small, it is possible to inexpensively produce duplex stainless steel suitable for building materials, and therefore the industrial value is extremely large.
第１図はオーステナイト相面積率（％）とレラクセーシ
ョン率の関係、第２図（Ａ）〜（Ｅ）は実施例１におけ
る材質調査結果を示すもので、（Ａ）は耐力（SP）、
（Ｂ）は引張り強さ（TS）、（Ｃ）は破断伸び（El）、
（Ｄ）はシャルピー吸収エネルギー（vEo）、（Ｅ）は
オーステナイト相面積分率（Ｆγ）をNi−Cr含有量との
関係で示した。FIG. 1 shows the relationship between the austenite phase area ratio (%) and the relaxation ratio, and FIGS. 2 (A) to (E) show the results of the material investigation in Example 1, where (A) is the yield strength (SP). ,
(B) is tensile strength (TS), (C) is elongation at break (El),
(D) shows the Charpy absorbed energy (vEo), and (E) shows the austenite phase area fraction (Fγ) in relation to the Ni-Cr content.
Claims (2)
つオーステナイト相面積率が20〜80％である建築建材用
二相ステンレス鋼。1. C: 0.10% or less by weight%, Si: 0.1 to 0.3%, Mn: 0.1 to less than 4.0%, Cr: 19.0 to 26.0%, Ni :: 1.0 to 6.0%, N: 0.05 to 0.40% Duplex stainless steel for use in building materials, which contains, and the balance is iron and inevitable impurities, and has an austenite phase area ratio of 20 to 80%.
りが鉄および不可避的不純物からなり、かつオーステナ
イト相面積率が20〜80％である建築建材用二相ステンレ
ス鋼。2. By weight%, C: 0.10% or less, Si: 0.1 to 0.3%, Mn: 0.1 to less than 4.0%, Cr: 19.0 to 26.0%, Ni: 1.0 to 6.0%, N: 0.05 to 0.40%, And Nb: 0.01 to 2.0%, Ti: 0.01 to 2.0%, V: 0.01 to 2.0%, and one or more of them, with the balance consisting of iron and inevitable impurities, and having an austenite phase area ratio. Duplex stainless steel for building materials which is 20-80%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1126665A JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1126665A JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02305940A JPH02305940A (en) | 1990-12-19 |
| JPH0768603B2 true JPH0768603B2 (en) | 1995-07-26 |
Family
ID=14940842
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1126665A Expired - Lifetime JPH0768603B2 (en) | 1989-05-22 | 1989-05-22 | Duplex stainless steel for building materials |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0768603B2 (en) |
Families Citing this family (19)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2789918B2 (en) * | 1992-03-03 | 1998-08-27 | 住友金属工業株式会社 | Duplex stainless steel with excellent weather resistance |
| KR100216683B1 (en) * | 1994-12-16 | 1999-09-01 | 고지마 마타오 | Duplex stainless steel excellent in corrosion resistance |
| AU2002242314B2 (en) * | 2001-10-30 | 2007-04-26 | Ati Properties, Inc. | Duplex stainless steels |
| WO2005073422A1 (en) | 2004-01-29 | 2005-08-11 | Jfe Steel Corporation | Austenitic-ferritic stainless steel |
| JP4760032B2 (en) * | 2004-01-29 | 2011-08-31 | Ｊｆｅスチール株式会社 | Austenitic ferritic stainless steel with excellent formability |
| JP4760031B2 (en) * | 2004-01-29 | 2011-08-31 | Ｊｆｅスチール株式会社 | Austenitic ferritic stainless steel with excellent formability |
| JP5021901B2 (en) * | 2005-02-28 | 2012-09-12 | Ｊｆｅスチール株式会社 | Austenitic and ferritic stainless steel with excellent intergranular corrosion resistance |
| JP5156293B2 (en) * | 2007-08-02 | 2013-03-06 | 新日鐵住金ステンレス株式会社 | Ferritic / austenitic stainless steel with excellent corrosion resistance and workability and manufacturing method thereof |
| CN101765671B (en) * | 2007-08-02 | 2012-01-11 | 新日铁住金不锈钢株式会社 | Ferritic-austenitic stainless steel excellent in corrosion resistance and workability and process for manufacturing the same |
| JP5213386B2 (en) * | 2007-08-29 | 2013-06-19 | 新日鐵住金ステンレス株式会社 | Ferritic / austenitic stainless steel sheet with excellent formability and manufacturing method thereof |
| JP5014915B2 (en) * | 2007-08-09 | 2012-08-29 | 日新製鋼株式会社 | Ni-saving austenitic stainless steel |
| TWI394848B (en) | 2007-10-10 | 2013-05-01 | Nippon Steel & Sumikin Sst | Two-phase stainless steel wire rod, steel wire, bolt and manufacturing method thereof |
| MX2010005670A (en) | 2007-11-29 | 2010-06-02 | Ati Properties Inc | Lean austenitic stainless steel. |
| DK2229463T3 (en) | 2007-12-20 | 2017-10-23 | Ati Properties Llc | Corrosion resistant lean austenitic stainless steel |
| PL2245202T3 (en) | 2007-12-20 | 2011-12-30 | Ati Properties Inc | Austenitic stainless steel low in nickel containing stabilizing elements |
| US8337749B2 (en) | 2007-12-20 | 2012-12-25 | Ati Properties, Inc. | Lean austenitic stainless steel |
| EP2093303A1 (en) * | 2008-09-04 | 2009-08-26 | Scanpump AB | Duplex Cast Steel |
| DE102012100908A1 (en) * | 2012-02-03 | 2013-08-08 | Klaus Kuhn Edelstahlgiesserei Gmbh | Duplex steel with improved notched impact strength and machinability |
| JP7334941B2 (en) * | 2019-08-02 | 2023-08-29 | 新報国マテリアル株式会社 | Duplex stainless steel casting |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE451465B (en) * | 1984-03-30 | 1987-10-12 | Sandvik Steel Ab | FERRIT-AUSTENITIC STAINLESS STEEL MICROLEGATED WITH MOLYBID AND COPPER AND APPLICATION OF THE STEEL |
-
1989
- 1989-05-22 JP JP1126665A patent/JPH0768603B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH02305940A (en) | 1990-12-19 |
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