JPS5913053A - Stainless steel with superior corrosion resistance, workability and weldability - Google Patents
Stainless steel with superior corrosion resistance, workability and weldabilityInfo
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- JPS5913053A JPS5913053A JP11950682A JP11950682A JPS5913053A JP S5913053 A JPS5913053 A JP S5913053A JP 11950682 A JP11950682 A JP 11950682A JP 11950682 A JP11950682 A JP 11950682A JP S5913053 A JPS5913053 A JP S5913053A
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Abstract
Description
【発明の詳細な説明】
本発明は耐食性、機械的性質及び溶接性の優れた安価な
ステンレス鋼に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to an inexpensive stainless steel with excellent corrosion resistance, mechanical properties, and weldability.
ステンレス鋼の用途が広がるにつれて、安価で耐食性が
よく、かつ薄板の加工性や、機械的性質のスクれたステ
ンレス鋼が要求されている。従来ステンレス鋼薄板はＳ
ｎ２３０４ （１８Ｃｒ−８Ｎｌ）と５ＵＳ４３０ （
１７Ｃｒ）鋼に代表されて来、たが用途の拡大は更に低
コストでのステンレス鋼薄板を要求している。As the uses of stainless steel expand, there is a demand for stainless steel that is inexpensive, has good corrosion resistance, is easy to work into thin plates, and has good mechanical properties. Conventional stainless steel thin plate is S
n2304 (18Cr-8Nl) and 5US430 (
17Cr) steel, and the expansion of its applications requires thin stainless steel sheets at even lower costs.
本発明者は高純化精錬によってステンレス鋼の耐食性が
大巾に向上することを見出し、これをもとに低Ｃｒであ
シながら１７Ｃｒ鋼に匹敵する耐食性を有する鋼材の開
発が可能であることを見出した。しかもこれらの低Ｃｒ
ステンレス鋼は軟質である麺め、従来ステンレス鋼で採
用されているゼンジミャー冷延にかぎらず、高生産性の
普通鋼用タンデム冷延においても容易に冷延出来、かつ
最終焼鈍も普通鋼用の高速連続焼鈍ラインで焼鈍可能な
ことを明らかにした。こうして、高純化精錬をポイント
にした低Ｃｒ化したステンレス鋼は普通鋼プロセスの製
造が可能となシ、生産速度が向上し、大巾にコストダウ
ン出来るという著しい利点があることが確められたが、
本発明者はさらに、■耐食性や耐誘性が１７％Ｃｒステ
ン４レス鋼と同等である、■薄板の加工性が１７％Ｃｒ
ステンレス鋼と同等以上である、■溶接性や溶接部の耐
食性等の特性が１７１０ｒ以上である、を目標特性とし
、製造について普通鋼と同様なプロセスによる生産をも
可能とした低Ｃｒステンレス鋼を提供すべく本発明を構
成したものである。The present inventor has discovered that the corrosion resistance of stainless steel can be greatly improved by high-purity refining, and based on this finding, it is possible to develop a steel material that is low in Cr but has corrosion resistance comparable to 17Cr steel. I found it. Moreover, these low Cr
Stainless steel is soft and can be easily cold rolled not only by Sendzimir cold rolling, which is conventionally used for stainless steel, but also by high-productivity tandem cold rolling for ordinary steel, and the final annealing is similar to that for ordinary steel. It was revealed that annealing is possible on a high-speed continuous annealing line. In this way, it was confirmed that low-Cr stainless steel, which is made with high purity refining, can be manufactured using the ordinary steel process, and has the remarkable advantage of increasing production speed and significantly reducing costs. but,
The inventor further found that: (1) Corrosion resistance and induction resistance are equivalent to 17% Cr stainless steel, and (2) Workability of thin plate is 17% Cr.
We aim to develop a low Cr stainless steel that is equivalent to or better than stainless steel, and has properties such as weldability and corrosion resistance of welded parts of 1710r or higher, and can be manufactured using the same process as ordinary steel. This is what the present invention is designed to provide.
以下に本発明の詳細な説明する。本発明者は９俤程度の
ＣＦから１９％程度まで巾広いＣｒ合金について検、肘
したが、目標とする醇記３要件を満たす合金はＣｒが１
１．５１を超え１５１以下で、かつ高純竺金（Ｃ＜、０
．０３０優、Ｓ＜０．ＱＯ２％、Ｐ≦０．０２０係、。The present invention will be explained in detail below. The present inventor has investigated and experimented with a wide range of Cr alloys, from about 9% CF to about 19% CF, but the alloy that satisfies the target 3 requirements has a Cr content of 1%.
more than 1.51 and less than 151, and high purity gold (C<,0
．． 030 excellent, S<0. QO2%, P≦0.020.
？り０．００１１＋１）で得られる９とが判、明した。? 9 obtained by 0.0011+1).
、まず、低Ｃｒ鋼の耐食性、耐誘性に対しては、
Ｃ２ｓ、ｐ、ｏの低減が必要である。Ｓ、を、２０ｐｐ
ｍ。First, regarding the corrosion resistance and induction resistance of low Cr steel,
It is necessary to reduce C2s, p, and o. S, 20pp
m.
望ましくは１．０．ｐｐｍＪｌ下に低減するとすぐ、、
７．た耐食性、耐誘性が得られる。、第、１図はこの様
子を示しているが、Ｓが２０ ｐｐｍ以下、でｓ １４
％のＣｒで１７ Ｔｏ Ｃｒステンレス鋼に匹敵すφ耐
誘性が得られる。０は５０ ｐｐｍ以下でなせれば炭（
ｇ物が析出しはじめると耐誘性が劣化する。Ｃｒが増、
加するとＣの固溶度が減少して粒界に炭化物を析出、す
る。Preferably 1.0. As soon as it is reduced below ppmJl,
7. It provides excellent corrosion resistance and resistance to corrosion. , Fig. 1 shows this situation, but when S is 20 ppm or less, s 14
% Cr provides φ induction resistance comparable to 17 To Cr stainless steel. 0 is charcoal (if it can be made below 50 ppm)
When g substances begin to precipitate, the induction resistance deteriorates. Cr increases,
When C is added, the solid solubility of C decreases and carbides are precipitated at grain boundaries.
第１図の■の場合がこのケ、−スでＣｒ１４＊を境に。In the case of ■ in Figure 1, the boundary is Cr14*.
耐食性、耐誘性が劣化する。Ｐは炭化物の析出を促進す
るので、Ｃと共にＣｒ量と次の関係式を満たす範囲に低
下させねばならない。Corrosion resistance and induction resistance deteriorate. Since P promotes the precipitation of carbides, it must be reduced together with C to a range that satisfies the following relational expression with the amount of Cr.
Ｃｒ ＋１００ （Ｃ＋Ｐ、 ）≦す
薄板の加工性及び溶接性、溶接部の耐食性、＠銹性の改
善においては高温で（α＋γ）組成にな（５）
る場合のｒの量が大きな役割シをはたしている、とのγ
がある量以上存在すると、変態が十分進み薄板のりジン
グ性及び深絞シ性（１値）を改良すると共に、溶接時の
冷却中に低Ｃの靭性や耐食性にスクれたマツシブマルテ
ンサイトを形成し、・溶接部の特性、耐食性も大巾に改
善される。このためにはＣ５；０．０２０％でγ、≧１
５％が必要である。In improving the workability and weldability of thin plates with Cr +100 (C+P, )≦, the corrosion resistance of welds, and the rust resistance, the amount of r plays a major role when the composition changes to (α+γ) at high temperatures (5). γ of ``Hatashiru''
When present in a certain amount or more, the transformation progresses sufficiently to improve the thin sheet lubricating properties and deep drawing properties (1 value), as well as to transform the matsive martensite, which has low C toughness and corrosion resistance, during cooling during welding.・The properties and corrosion resistance of the welded part are greatly improved. For this, C5; γ at 0.020%, ≧1
5% is required.
この際の５．ｒｐはＣａ５ｔｒｏによる以下の式で足義
したものである。5. rp is defined by the following formula by Ca5tro.
、第２図は低Ｃ＋ Ｆｍ−Ｃｒ合金（Ｃ５０，００２１
゜Ｎ≦０．０２％ −Ｃｒ ９〜１ ｙｓ 、Ｎｌ Ｏ
，１％）Ｏｒｐと７との関係を示している。, Figure 2 shows the low C+ Fm-Cr alloy (C50,0021
゜N≦0.02% -Cr 9~1 ys, NlO
, 1%) shows the relationship between Orp and 7.
ｒｐ ＝ ４２００＋４７ＯＮ＋２３Ｎｌ＋９Ｃｕ＋
７Ｍｎ−１１，５Ｃｒ、−１１，５８１−１２Ｍｏ−２
３Ｖ−４７Ｎｂ−４９ＴＩ−５２Ａｔ＋１８９゜
なお、ここでＭｏ ＋ Ｖ 、 Ｎｂ ＃ Ｔｉ等は選
択添加元素である・。rp=4200+47ON+23Nl+9Cu+
7Mn-11,5Cr, -11,581-12Mo-2
3V-47Nb-49TI-52At+189° Here, Mo + V, Nb #Ti, etc. are selective addition elements.
以上、述べた様に成分を制御することで、特性上必要な
要件は満たされる。最後にＣｒ１ｌについて述べると、
Ｃｒ量が１５％をこえるとｒ、が低下し、（６）
粒界に炭化物が析出し、粒界より発銹しやすくなる。又
溶接部で粒界腐食や発銹が著しくなる。したがってＣｒ
は１５係以下が望ましい。又耐食性の向上のためには１
１．４１以上が必要である。By controlling the components as described above, the necessary requirements for characteristics can be satisfied. Finally, regarding Cr1l,
When the amount of Cr exceeds 15%, r decreases, and (6) carbides precipitate at grain boundaries, making it easier to rust than at grain boundaries. In addition, intergranular corrosion and rusting occur at welded parts. Therefore, Cr
It is desirable that the number is 15 or less. Also, in order to improve corrosion resistance, 1
1.41 or higher is required.
以下に本発明鋼の添加成分の限定理由を述べる。The reasons for limiting the additive components of the steel of the present invention will be described below.
Ｃは低Ｃｒステンレス鋼において相変態を生せしめるが
、多過ぎると炭化物として析出し、粒界腐食抵抗をそこ
ない、耐錆性を低下せしめる。又薄板の加工性の点でも
低い方が望壕しく、したがって０．０３％以下でかつＣ
ｒ 、 Ｐとの関連でＣｒ ＋１００［Ｃ＋Ｐ］≦１８
を満たすことが必要である。C causes phase transformation in low Cr stainless steel, but if too much C precipitates as carbides, impairing intergranular corrosion resistance and lowering rust resistance. In addition, in terms of workability of the thin plate, it is better to have a lower C.
Cr +100[C+P]≦18 in relation to r, P
It is necessary to satisfy the following.
Ｓは低Ｃｒステンレス鋼の耐錆性を向上し、低ければ低
い程好ましく０．００２０％以下、望ましくはｏ、ｏｏ
ｔｏ＊以下であることが必要である。S improves the rust resistance of low Cr stainless steel, and the lower it is, the more preferably it is 0.0020% or less, preferably o, oo
It is necessary to be less than or equal to to*.
Ｐは低い程低Ｃｒステンレス鋼の耐錆性を増す。The lower P increases the rust resistance of low Cr stainless steel.
したがってｐく０．０２０１であることが必要である。Therefore, it is necessary that p is 0.0201.
又炭化物の析出を促進するので、ＣとＣｒの量との関連
で次の関係を満たさねばならない。Furthermore, since it promotes the precipitation of carbides, the following relationship must be satisfied in relation to the amounts of C and Cr.
Ｃｒ ＋１００（Ｃ＋Ｐ）＜１８
０は介在物として、耐錆性を劣化させる。特にＳ＋Ｐを
低減した合金で悪影響が大きく、０．００５０チ以下に
しなければならない。Cr +100(C+P)<180 acts as inclusions and deteriorates rust resistance. In particular, alloys with reduced S+P have a large negative effect and must be kept at 0.0050 or less.
Ｃｒは上述の如くステンレス鋼の必須元素で耐食性を増
す。Ｃｒ１１．５’％以下では耐食性が不十分である。As mentioned above, Cr is an essential element of stainless steel and increases corrosion resistance. If Cr is 11.5'% or less, corrosion resistance is insufficient.
Ｃｒの上限は多くの点で規制される。Ｃｒが高くなると
炭化物を析出しやすくなり耐誘性９粒界腐食性を劣化さ
せる。したがってＣ，Ｐとの関連で、Ｃｒ ＋ １００
ＣＣ十Ｐ ）＜１８で規制される。又薄板の加工性、
溶接性の点から高温で（α＋γ）相を生ぜしめる必要が
あシ、ｒポテンシャル、γ。The upper limit of Cr is regulated in many ways. When the Cr content increases, carbides tend to precipitate, which deteriorates the resistance to intergranular corrosion. Therefore, in relation to C and P, Cr + 100
CC0P ) < 18. Also, the workability of thin plates,
From the viewpoint of weldability, it is necessary to generate the (α+γ) phase at high temperature, r potential, γ.
を次式によシ規定する。is defined by the following equation.
γｐ ＝４２０ Ｃ＋ ４７ ＯＮ＋２３ Ｎｋ ＋９
Ｃｕ ＋ ７ Ｍｎ １ｌ−５Ｃｒ−１１，５８１
−１２Ｍｏ−４７Ｎｂ−４９ＴＩ−５２ＡＬ＋１８９≧
１５チ
したがってＣｒ１５％以下でなおかつ上記の規制が必要
となる。γp =420 C+ 47 ON+23 Nk +9
Cu + 7 Mn 1l-5Cr-11,581
-12Mo-47Nb-49TI-52AL+189≧
15%, therefore, it is necessary to keep the Cr at 15% or less and to comply with the above regulations.
Ｓｔは脱酸用及び耐食性向上の点で必要であるが硬化作
用を有するので２チ以下とした。St is necessary for deoxidation and improving corrosion resistance, but it has a hardening effect, so it was set to 2 or less.
Ｍｎは脱酸用及び機械的性質の点で必要であるが、耐食
性には低い程よく従って０．５チ以下とした。Mn is necessary for deoxidation and mechanical properties, but the lower the better for corrosion resistance, so it was set to 0.5 or less.
Ｎｌは機械的性質や溶接特性の向上、耐食性の向上に好
ましいが、硬化させるので１チ以下とした。Nl is preferable for improving mechanical properties, welding properties, and corrosion resistance, but since it causes hardening, the content was set to 1 or less.
Ｎは、耐食性や機械的性質にさはど影響しない。N does not significantly affect corrosion resistance or mechanical properties.
したがってすでに述べたγ、のコントロールを目的に０
．０５％以下とした。これ以上では硬化が大きくなる。Therefore, for the purpose of controlling γ, which was already mentioned, 0
．． 05% or less. If it exceeds this range, hardening will increase.
Ａｔは、薄板の加工性向上、脱酸用として有効である。At is effective for improving the processability of thin plates and for deoxidizing.
しかし、０．２係を超えると作用効果、が飽和するので
０．２係以下とした。However, if the coefficient exceeds 0.2, the effect will be saturated, so the coefficient is set to 0.2 or less.
Ｍｏ Ｔ Ｃｕ ＋ Ｔｌ 、Ｎｂ ｒ ｖ等は耐食性
ノ向上ニ、又Ｔｌ 、 Ｎｂ 、 Ｂ 、 Ｖ等は薄板
の加工性の向上に有効である。しかしこれらの合金元素
は硬化作用を有し、したがってＭｏ５１％、 Ｃｕ≦０
．５１．ＴＩ≦０．３％ ＃ ＮｂＳ２．３％ 、ＶＳ
２．７％＊Ｂ≦ｏ、ｏｔｓの範囲で用途によって、１種
又は２種以上選択添加することが出来る。ただし、特に
軟化と再結晶を容易にし、高生産性を目的とする場合に
は、主要合金元素の添加量全体も規制すべきで、Ｃｒ／
１５ ＋ （Ｎｌ＋Ｍｏ＋Ｃｕ）＋４（ＴＩ＋Ｎｂ）＜
３５ｂであることが必要である。Mo T Cu + Tl, Nbrv, etc. are effective for improving corrosion resistance, and Tl, Nb, B, V, etc. are effective for improving workability of thin plates. However, these alloying elements have a hardening effect, so Mo51%, Cu≦0
．． 51. TI≦0.3% #NbS2.3%, VS
Depending on the application, one or more types can be selectively added within the range of 2.7%*B≦o, ots. However, especially when the purpose is to facilitate softening and recrystallization and to achieve high productivity, the total amount of major alloying elements added should also be regulated, and Cr/
15 + (Nl+Mo+Cu)+4(TI+Nb)<
35b.
（９） 以下に本発明の実施例について説明する。(9) Examples of the present invention will be described below.
通常のステンレス鋼溶製プロセスであるＬＤ転炉とＶＡ
Ｃ処理法で、溶製したが、低Ｃ化、低Ｓ化。LD converter and VA, which is a normal stainless steel melting process
It was produced using the C treatment method, but the C and S were reduced.
低Ｐ化について特に留意し、取鍋におかて、フラックス
のインジェクションを実施した。又Ａｔによる脱酸を十
分性なって００低減を実施した。本発明鋼の成分例は第
１表鋼番■〜■の通シである。Particular attention was paid to low P, and flux injection was carried out in a ladle. In addition, 00 reduction was carried out to ensure that deoxidation by At was sufficient. Examples of the composition of the steel of the present invention are steel numbers ① to ② in Table 1.
その後連続鋳造を経て通常通υ熱間圧延し、巻取り後、
熱延板焼鈍を行なわずに酸洗し、鋼、番■。After that, after continuous casting, regular hot rolling and winding,
Hot-rolled plate pickled without annealing, steel, number ■.
■はステンレス工程のゼンジミャー冷延−焼鈍・酸洗ラ
インを通し、一方で調香■〜■につぃては普通鋼冷延・
焼鈍工程であるタンデム冷延連続焼−叫ラインを通した
。この際焼鈍条件は８５０℃１分以下で露点を一４０℃
とした。上記各工程を経 。■ is passed through the Sendzimir cold rolling, annealing, and pickling line in the stainless steel process, while ordinary steel cold rolling,
It passed through a tandem cold rolling continuous annealing line which is an annealing process. At this time, the annealing conditions were 850℃ for 1 minute or less, and the dew point was -40℃.
And so. After going through each of the above steps.
て得られた製品板の機械的性質を調査した。なお比較鋼
としては低Ｃ−１２Ｏｒ−Ｔｌ系であって従来よりタン
デム連続焼鈍工程で製造している鋼種と通常のＳＵＳ
４３０鋼とをゼンジミャー冷延と焼鈍・酸洗のステンレ
ス鋼工程で処理した。The mechanical properties of the resulting product plates were investigated. The comparative steels are a low C-12Or-Tl type steel that is conventionally manufactured using a tandem continuous annealing process and ordinary SUS.
430 steel was processed through the stainless steel process of Sendzimir cold rolling, annealing and pickling.
結果は第２表の通シである。耐錆性については（１０）
すでに述べた０、 ５４ ＮａＣｔ＋ ０．２ ％ Ｈ
２Ｏ２液で３０℃で２４時間＠霧したときの発銹程度で
評価した。比較鋼がＧランク、Ｅランクであるのに対し
て、本発明鋼は低ＯｒにもかかわらすＡ−Ｄランクの耐
誘性を示、シ、すぐれた特性を示した。又薄板の加工性
を薄板製品によｊ５ ＪＩＳ ５号引張試験片で調査し
た結果、普通鋼工程で製造した調香■〜■とステンレス
工程で製造した調香■とも、比較鋼■で示した８ＵＳ
４３０クラスの特性を上まわっている。又冷延後の再結
晶条件も調香■〜■までか８５０℃×１分以内の条件で
再結晶完了することを示してφる。又本発明鋼は溶接部
の耐誘性に関しても比較鋼よシすぐれた特性を示した。The results are shown in Table 2. Regarding rust resistance, (10) already mentioned 0, 54 NaCt + 0.2% H
Evaluation was made based on the degree of rusting when fogged with 2O2 solution at 30°C for 24 hours. While the comparative steels were ranked G and E, the steel of the present invention exhibited resistance to induction of ranks A-D despite its low Or, and exhibited excellent properties. In addition, as a result of investigating the workability of thin sheets using J5 JIS No. 5 tensile test pieces using thin sheet products, it was found that both the perfumes ■ to ■ manufactured using the ordinary steel process and the perfume ■ manufactured using the stainless steel process were compared to the comparative steel ■. 8US
The characteristics exceed those of the 430 class. The recrystallization conditions after cold rolling also indicate that recrystallization is completed within 850° C. for 1 minute from aroma adjustment ① to ②. The steel of the present invention also exhibited superior properties to the comparative steels in terms of induction resistance of welded parts.
１１１１ ゝゝ１ （１１） （１３）1111 ゝゝ1 (11) (13)
第１図は０．５ ％ ＮａＣ１＋ ０．２４ Ｈ２０□
液、（３０℃）を２４時間噴霧した場合の発銹程度に対
するＣｒ量及びＣ量、Ｓ量の影響を示した図、第２図は
低Ｃ２Ｆｅ−Ｃｒ合金のγ、と薄板の７値の関係を示し
た図である。
（１４）
碍柩 概
牟欅＼へ八へFigure 1 shows 0.5% NaC1+ 0.24 H20□
Figure 2 shows the effects of Cr content, C content, and S content on the degree of rusting when a liquid (30°C) is sprayed for 24 hours. It is a diagram showing the relationship. (14) 碍欩 ＼Hehachi
Claims (3)
ｌ：２．０％以下、Ｍｎ ： ０．５ ％以下、Ｐ ：
０．０２０％以下、８０．００２％以下、Ｃｒ ：１
１．５％〜１５チ、Ｎｉ：１％以下、ＡＬ：０．２％以
下、Ｎ：０．０５％以下、Ｏ：ｏ、ｏｏｓ％以下を含み
、残部は鉄及び不可避の不純物から成ると共に、 Ｃｒ＋１００（Ｃ＋Ｐ）６１８％ ７” ｐ ” ４２０ Ｃ＋ ４７０ Ｎ ＋ ２３
Ｎｉ ＋ ７ ＲＩＩｎ−１１，５Ｃｒ−１１，５Ｓｉ
−５２Ａｔ＋１８９≧１５チなる関係式を満すことを特
徴とする耐食性、加工性及び溶接特性のすぐれたステン
レス鋼。(1) Weight/4 cents, C: 0.030 m or less, S
L: 2.0% or less, Mn: 0.5% or less, P:
0.020% or less, 80.002% or less, Cr:1
Contains 1.5% to 15%, Ni: 1% or less, AL: 0.2% or less, N: 0.05% or less, O: o, oos% or less, and the remainder consists of iron and inevitable impurities. , Cr+100 (C+P) 618% 7"p" 420 C+ 470 N+23
Ni + 7 RIIn-11,5Cr-11,5Si
A stainless steel with excellent corrosion resistance, workability, and welding properties, which satisfies the following relational expression: -52At+189≧15.
：２．０％以下、Ｍｎ ： ０．５ ％以下、Ｐ：０．
０２０係以下、Ｓ ： ０．００２％以下、Ｃｒ ：
１１．５％〜１５％、Ｎｉ ： １％以下、ｈｔ：ｏ、
２９６以下、Ｎ：０．０５’％以下、ｏ ： ｏ、ｏｏ
ｓｓ以下およびＭｏ １ ％以下、ＣｕＯ０５係以下、
Ｔｌ Ｏ，’３多以下、ＮｂＯ，３係以下、ｖＯ４７チ
以下、ＢＯ３０１チ以下の１種又は２種以上を含み、残
部は鉄及び不可避の不純物から成ると共に、 Ｏｒ＋’１００Ｘ（Ｃ＋Ｐ）≦１８％ ｒ ＝４２０Ｃ＋４７ＯＮ＋２３Ｎｌ＋９Ｃｕ＋７Ｍ
ｎ−１１，５Ｃｒ−１１，５Ｓｉ−１２Ｍｏ−４７Ｎｂ
−４９ＴＩ −５２Ａｔ＋１８９≧１５チ なる関係式を満すことを特徴とする耐食性、加工性及び
溶接待′性のすぐれたステンレス鋼。(2) In weight percent, C: 0.030% or less, st
: 2.0% or less, Mn: 0.5% or less, P: 0.
020 or less, S: 0.002% or less, Cr:
11.5% to 15%, Ni: 1% or less, ht:o,
296 or less, N: 0.05'% or less, o: o, oo
ss or less and Mo 1% or less, CuO05 or less,
Contains one or more of the following: Tl O, 3 or less, NbO, 3 or less, vO 47 or less, BO 301 or less, the remainder consisting of iron and unavoidable impurities, and Or + '100X (C + P) ≦ 18 %r=420C+47ON+23Nl+9Cu+7M
n-11,5Cr-11,5Si-12Mo-47Nb
-49TI -52At+189≧15 A stainless steel with excellent corrosion resistance, workability and weldability, characterized by satisfying the following relational expression: -49TI -52At+189≧15.
ｌ：２，０％以下、Ｍｎ ： ０．５％以下、Ｐ ：
０．０２０チ以下、Ｓ ： ０．００２ｑＩｂ以下、Ｃ
ｒ ： １１．５９６〜１５ ％ 。 Ｎ１：１チ以下、Ａｔ： ０．２係以下、Ｎ：０．０５
チ以乍、Ｏ： ０．００５１以下およびＭｏ １％以下
、ＣｕＯ，５％以下、Ｔ１０．３１以下、Ｎｂ Ｏ，３
１以下、ＶＯ，７チ以下、Ｂｏ、０１チ以下の１種又は
２種以上を含み、残部は鉄及び不可避の不純物から成る
と共に、 Ｃｒ ＋ １００Ｘ（Ｃ−１−Ｐ）≦１８係ｒ ＝４
２００＋４７ＯＮ＋２３Ｎｌ＋９Ｃｕ＋７Ｍｎ−１１，
５Ｃｒ＝１ｔ、５ｓｔ−０２，。−４゜Ｎｂ−４９Ｔ
Ｉ−５゜。□、、８゜≧１５チ Ｃｒ／ｉ５ ＋（Ｎ１＋Ｍｏ＋Ｃｕ）＋４ （ＴＩ＋Ｎ
ｂ）＜３ ％なる関係式を満すことを特徴とする耐食性
、加工性及び溶接特性のすぐれたステンレス鋼。(3) Weight (- cents, c: o, oao 俤 or less, S
L: 2.0% or less, Mn: 0.5% or less, P:
0.020q or less, S: 0.002qIb or less, C
r: 11.596-15%. N1: 1 inch or less, At: 0.2 section or less, N: 0.05
Chi and O: 0.0051 or less and Mo 1% or less, CuO, 5% or less, T10.31 or less, Nb O, 3
1 or less, VO, 7 or less, Bo, 01 or less, the remainder consists of iron and unavoidable impurities, and Cr + 100X (C-1-P)≦18 coefficient r = 4
200+47ON+23Nl+9Cu+7Mn-11,
5Cr=1t, 5st-02,. -4゜Nb-49T
I-5°. □,,8゜≧15chi Cr/i5 + (N1+Mo+Cu)+4 (TI+N
b) Stainless steel with excellent corrosion resistance, workability and welding properties, which satisfies the relational expression <3%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11950682A JPS5913053A (en) | 1982-07-09 | 1982-07-09 | Stainless steel with superior corrosion resistance, workability and weldability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP11950682A JPS5913053A (en) | 1982-07-09 | 1982-07-09 | Stainless steel with superior corrosion resistance, workability and weldability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS5913053A true JPS5913053A (en) | 1984-01-23 |
| JPH0435551B2 JPH0435551B2 (en) | 1992-06-11 |
Family
ID=14762941
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP11950682A Granted JPS5913053A (en) | 1982-07-09 | 1982-07-09 | Stainless steel with superior corrosion resistance, workability and weldability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS5913053A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6173864A (en) * | 1984-09-17 | 1986-04-16 | Kawasaki Steel Corp | Martensitic stainless steel sheet having superior oxidation resistance and workability and its manufacture |
| JPS63213640A (en) * | 1987-02-28 | 1988-09-06 | Nippon Stainless Steel Co Ltd | Stainless steel for heat transfer pipe-supporting plate in steam generator |
| JPH0499151A (en) * | 1990-08-03 | 1992-03-31 | Nkk Corp | Ferritic stainless steel excellent in press formability and surface characteristic and its production |
| JP2005226129A (en) * | 2004-02-13 | 2005-08-25 | Nippon Steel & Sumikin Stainless Steel Corp | Method for manufacturing ferritic stainless steel cast slab |
| US8860280B2 (en) | 2011-04-01 | 2014-10-14 | Denso Corporation | Rotor for electric rotating machine and method of manufacturing the same |
-
1982
- 1982-07-09 JP JP11950682A patent/JPS5913053A/en active Granted
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6173864A (en) * | 1984-09-17 | 1986-04-16 | Kawasaki Steel Corp | Martensitic stainless steel sheet having superior oxidation resistance and workability and its manufacture |
| JPH0448866B2 (en) * | 1984-09-17 | 1992-08-07 | Kawasaki Steel Co | |
| JPS63213640A (en) * | 1987-02-28 | 1988-09-06 | Nippon Stainless Steel Co Ltd | Stainless steel for heat transfer pipe-supporting plate in steam generator |
| JPH0524224B2 (en) * | 1987-02-28 | 1993-04-07 | Nippon Sutenresu Kk | |
| JPH0499151A (en) * | 1990-08-03 | 1992-03-31 | Nkk Corp | Ferritic stainless steel excellent in press formability and surface characteristic and its production |
| JP2005226129A (en) * | 2004-02-13 | 2005-08-25 | Nippon Steel & Sumikin Stainless Steel Corp | Method for manufacturing ferritic stainless steel cast slab |
| JP4624691B2 (en) * | 2004-02-13 | 2011-02-02 | 新日鐵住金ステンレス株式会社 | Method for producing ferritic stainless steel slab |
| US8860280B2 (en) | 2011-04-01 | 2014-10-14 | Denso Corporation | Rotor for electric rotating machine and method of manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0435551B2 (en) | 1992-06-11 |
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