JP3446449B2 - Ferritic stainless steel sheet with excellent ridging resistance - Google Patents
Ferritic stainless steel sheet with excellent ridging resistanceInfo
- Publication number
- JP3446449B2 JP3446449B2 JP03221896A JP3221896A JP3446449B2 JP 3446449 B2 JP3446449 B2 JP 3446449B2 JP 03221896 A JP03221896 A JP 03221896A JP 3221896 A JP3221896 A JP 3221896A JP 3446449 B2 JP3446449 B2 JP 3446449B2
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- steel sheet
- ferritic stainless
- ridging resistance
- ridging
- 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.)
- Expired - Lifetime
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- Heat Treatment Of Sheet Steel (AREA)
Description
【発明の詳細な説明】
【０００１】
【発明の属する技術分野】本発明は耐リジング性に優れ
たフェライト系ステンレス鋼板に関する。
【０００２】
【従来の技術】フェライト系ステンレス鋼は耐食性や耐
酸化性に優れた材料であり、種々な産業分野で広く利用
されている。しかしながら鋼板の状態でプレス加工等に
より深絞り加工されると、リジングと呼ばれる肌荒れ状
の表面欠陥が生じ易いという欠点を有しており、従来、
深絞り加工等の厳しい加工が施される用途には不向きで
あるとされていた。
【０００３】これに対して、耐リジング性改善を目的と
した種々な技術が開示されている。それらは大別する
と、（１）成分元素に着目した技術、（２）製造プロセ
スに着目した技術に分類される。
（１）成分元素に着目した技術に関しては、特開昭５２
−０２４９１３号公報に、Ｃ：０．０３〜０．０８ｗｔ
％、Ｎ≦０．０１ｗｔ％、Ｓ≦０．００８ｗｔ％、Ｐ≦
０．０３ｗｔ％、Ｓｉ≦０．４ｗｔ％、Ｍｎ≦０．５ｗ
ｔ％、Ｎｉ≦０．３ｗｔ％、Ｃｒ：１５〜２０ｗｔ％、
Ａｌ：Ｎ×２〜０．２ｗｔ％を含有し、残部Ｆｅ及び不
可避的不純物からなる加工性に優れたフェライト系ステ
ンレス鋼が開示されている。
【０００４】（２）製造プロセスに着目した技術に関し
ては特開昭５５−１４１５２２号公報に、Ａｌを含有す
るフェライト系ステンレス鋼スラブを９５０℃以上１１
００℃以下の温度に保持した後熱延を施すことを特徴と
するリジングの著しく少ないフェライト系ステンレス鋼
の製造方法が開示されている。
【０００５】
【発明が解決しようとする課題】従来開示されているこ
れらの技術では、耐リジング性の効果は十分とはいえ
ず、ただ単に、従来開示されていた素材成分や熱延条件
だけでは耐リジング性の良好なフェライト系ステンレス
鋼を安定的に得ることは困難であった。このような現状
に鑑み、本発明者等は長年に亘り、鋭意研究を行った結
果、耐リジング性改善に対して鋼中の析出物の量と大き
さとをコントロールすることが非常に有効であることを
見出すに至った。
【０００６】本発明はこの知見に基づき、耐リジング性
に優れたフェライト系ステンレス鋼板を提供することを
目的とする。
【０００７】
【課題を解決するための手段】本発明は、１１ｗｔ％以
上のＣｒを含有するフェライト系ステンレス鋼板におい
て、重量比でＴｉが０．０９〜０．４１％でかつＴｉ／
（Ｃ＋Ｎ＋Ｓ）≧３で、鋼板の平均結晶粒径をｄmeanと
した時に粒径３μｍ以下のＴｉの炭化物、窒化物及び硫
化物の析出物が（ｄmean）2 あたり１個以上存在し、Ｔ
ｉの炭化物、窒化物及び硫化物の析出物の体積割合が
０．５％以下であることを特徴とする耐リジング性に優
れたフェライト系ステンレス鋼板を提供する。
【０００８】
【発明の実施の形態】以下、本発明をさらに詳しく説明
する。
Ｃｒ：Ｃｒは耐食性に非常に有効な元素である。その効
果は、１１ｗｔ％以上で顕著となるため、下限は１１ｗ
ｔ％とした。上限については特に規定はしないが、５０
重量ｗｔ％を越えると熱間強度が大きくなるばかりか冷
延性も低下するため、製造しずらくなるので、好ましく
は５０ｗｔ％以下が好ましい。
【０００９】Ｔｉ：Ｔｉは、本発明に非常に重要な元素
である。後述する如く、析出物の大きさ、分布を制御
し、冷延後の焼鈍時の再結晶時に、フェライト単相鋼に
発生し易いリジング現象の原因となるコロニーやバンド
状組織成長を阻止することに寄与する。特に、Ｔｉの硫
化物、炭化物、窒化物の生成が有効である。図１に、１
６．４ｗｔ％Ｃｒ鋼（Ｆｅ−１６．４ｗｔ％Ｃｒ−０．
４ｗｔ％Ｓｉ−０．２ｗｔ％Ｍｎ−０．００５ｗｔ％Ｃ
−０．００９ｗｔ％Ｎ−０．００３ｗｔ％Ｎ−０．３０
ｗｔ％Ｐ−０．５０ｗｔ％Ｍｏ）についてＴｉ量を種々
変化させたときの耐リジング性に及ぼすＴｉ／（Ｃ＋Ｎ
＋Ｓ）の影響を示すが、Ｔｉ／（Ｃ＋Ｎ＋Ｓ）が３以上
で耐リジング性が著しく優れることがわかる。
【００１０】粒径３μｍ以下の（炭化物＋窒化物＋硫化
物）が鋼板の平均結晶粒径をｄmeanとした時に
（ｄmean）2 あたり１個以上存在し、これらの体積割合
が０．５％以下であることが本発明の基幹をなす技術で
ある。粒径３μｍ以下の析出物が冷延後の再結晶時に
（１００）コロニーやバンド状組織を生成するのを阻止
し、リジング発生を抑制するからである。この時に、析
出物の大きさ（粒径）は３μｍ以下でなければならな
い。これは、３μｍを越えると再結晶時に有効に（１０
０）コロニーやバンド状組織の生成を阻止することがで
きず、本発明の効果が得られないからである。
【００１１】図２にＦｅ−１８．１ｗｔ％Ｃｒ−０．４
ｗｔ％Ｍｎ−０．００９ｗｔ％Ｃ−０．０１２ｗｔ％Ｎ
−０．００３ｗｔ％Ｓ−０．２０ｗｔ％Ｔｉの（炭化物
＋窒化物＋硫化物）個数／（ｄmean）2 に対するリジン
グ評点を示した。図２に示すように、耐リジング性改善
の観点からは、析出物は、平均結晶粒径をｄmeanとした
ときに、（ｄmean）2 あたり１個以上なければならな
い。それ未満では、析出物が耐リジング性改善には有効
に作用しないからである。
【００１２】また、これら析出物の量は体積比で０．５
％以下でなければならない。０．５％を越えると、耐食
性とりわけ耐孔食性の低下が生じ易くなるからである。
ここで、析出物については、炭化物、窒化物、硫化物の
単独であろうと複合であろうと本発明の条件を満たして
おれば限定はしない。
【００１３】フェライト系ステンレス鋼には、耐食性や
耐酸化性、機械的性質等種々な特性を改善する目的か
ら、Ｓｉ、Ｍｎ、Ａｌ、Ｍｏ、Ｎｉ、Ｃｕ、Ｎｂ、Ｖ、
Ｗ、Ｃａ、Ｍｇ、Ｂ、Ｐ、Ｔａ、Ｚｒなど様々な元素を
添加したり、あるいは、不可避的不純物としてこれら元
素やＯ、Ａｓ、Ｂｉ、Ｓｂなどが混入する。基本的に本
発明の条件が満足されればこれらの成分の添加あるいは
混入は何ら問題はないので、限定はしない。
【００１４】本発明の耐リジング性に優れたフェライト
系ステンレス鋼板は、一般的には、工業的に次のような
方法によって製造される。溶製後連続鋳造法により厚み
が１６０〜２６０ｍｍ程度のスラブを得る。この時に、
炭化物、窒化物、硫化物の析出形態（大きさ、分布）の
点から好ましくは高速鋳造（例えば鋳造速度が０．７ｍ
／ｍｉｎ以上）がよい。その後スラブは、熱間圧延によ
り板厚１．５ｍｍから６ｍｍ程度の熱延鋼帯にされる。
このときに、本願の発明のポイントになる析出物の大き
さと分布の点から、スラブ均熱温度は１２００℃以下が
好ましい。また、ＴｉＣや、ＴｉＮの微細析出の観点か
ら、熱延時の粗圧延終了温度は１０５０℃から９５０℃
の範囲が好ましく、また、粗圧延での最低１パス以上に
ついて圧下率が３０％以上であることがよい。一般的に
得られた熱延鋼帯には、再結晶焼鈍が施されるが、その
温度は、合金元素量により異なっているものの、本願の
効果を得るためには、１１５０℃を越えると、熱延時に
析出した、炭・窒化物の粗大化あるいは再固溶が生じ易
くなるので、１１５０℃以下であることが好ましい。な
お、熱延鋼帯の焼鈍は、必要不可欠ではなく、そのま
ま、冷延を施しても本願は達成される。冷延鋼板として
使用されるときには、さらに、冷間圧延・再結晶焼鈍が
施される。とくに、再結晶焼鈍については、本願の効果
である、析出物形態（大きさと分布）の点から、１０５
０℃以下であることが好ましく、また、平均結晶粒径も
１５０μｍ以下であることがよい。
【００１５】
【実施例】以下に本発明を実施例に基づいて説明する。
表１に示す種々の合金を実験室的に３０ｋｇ溶製し、公
知の熱間圧延により板厚４ｍｍの熱延板とした。得られ
た熱延板を再結晶焼鈍後、脱スケールし、板厚０．７ｍ
ｍまで冷延後再結晶焼鈍を施し、冷延焼鈍板を作製し
た。
【００１６】耐リジング性の評価は、圧延方向に２０ｗ
ｔ％引張歪を与えた後の鋼板表面に発生するリジングの
程度で評価した。析出物の観察はＳＥＭにより行い、１
００視野観察し個数を測定した。また、平均結晶粒径
は、光学顕微鏡による切断法により求めた。両者から、
（ｄmean）2 面積当たり粒径３μｍ以下の析出物個数を
求めた。耐リジング性評価結果を表２に示す。本発明例
は、いずれの場合も、耐リジング性に著しく優れている
ことがわかる。一方、３μｍ以下の析出物の個数が少な
いか、あるいはＴｉ／（Ｃ＋Ｎ＋Ｓ）が３未満であると
耐リジング性が劣っていることがわかる。
【００１７】
【表１】
【００１８】
【表２】【００１９】
【発明の効果】本発明によれば、Ｔｉ／（Ｃ＋Ｎ＋Ｓ）
が３以上であることと、平均結晶粒径をｄmeanとしたと
きに、粒径３μｍ以下の炭化物・硫化物・窒化物が（ｄ
mean） 2 あたり１個以上存在させることにより、フェラ
イト系ステンレス鋼の耐リジング性を著しく改善するこ
とができるようになった。DETAILED DESCRIPTION OF THE INVENTION
[0001]
TECHNICAL FIELD The present invention is excellent in ridging resistance
Ferritic stainless steel sheet.
[0002]
2. Description of the Related Art Ferritic stainless steel has corrosion resistance and
Excellent oxidizing material, widely used in various industrial fields
Have been. However, for press working etc. in the state of steel sheet
When deep drawing is performed, rough surface called ridging
Has the drawback that surface defects tend to occur.
Not suitable for applications where severe processing such as deep drawing is performed
It was supposed to be.
On the other hand, with the aim of improving ridging resistance,
Various techniques have been disclosed. They are roughly divided
And (1) technology focusing on component elements, and (2) manufacturing process
Technology that focuses on
(1) Japanese Patent Laid-Open No.
-024913, C: 0.03 to 0.08 wt
%, N ≦ 0.01 wt%, S ≦ 0.008 wt%, P ≦
0.03wt%, Si ≦ 0.4wt%, Mn ≦ 0.5w
t%, Ni ≦ 0.3 wt%, Cr: 15 to 20 wt%,
Al: contains N × 2 to 0.2 wt%, the balance being Fe and
Ferritic stainless steel with excellent workability
Stainless steel is disclosed.
(2) Regarding technology focusing on the manufacturing process
Japanese Patent Application Laid-Open No. 55-141522 discloses that
Ferritic stainless steel slab over 950 ° C
It is characterized by applying hot rolling after holding at a temperature below 00 ° C.
Ferritic stainless steel with extremely low ridging
Is disclosed.
[0005]
DISCLOSURE OF THE INVENTION Problems to be Solved by the Invention
With these technologies, the effect of ridging resistance is sufficient.
In addition, simply, conventionally disclosed material components and hot rolling conditions
Ferritic stainless steel with good ridging resistance alone
It was difficult to obtain steel stably. Such current situation
In view of this, the present inventors have conducted intensive research for many years.
As a result, the amount and size of precipitates in steel for improving ridging resistance
That controlling sato is very effective
I came to find it.
[0006] Based on this finding, the present invention provides ridging resistance.
To provide excellent ferritic stainless steel sheet
Aim.
[0007]
Means for Solving the Problems The present invention provides a method for producing a semiconductor device having an
Above Cr-containing ferritic stainless steel sheet
And the weight ratioTi is 0.09 to 0.41% andTi /
When (C + N + S) ≧ 3, the average grain size of the steel sheet is dmeanWhen
When the particle size is 3μm or lessTicarbide,Nitrideas well asSulfuric acid
monsterPrecipitateIs (dmean)Two One or more perT
i'scarbide,Nitrideas well asSulfidePrecipitateVolume ratio of
0.5%Excellent ridging resistance characterized by the following
To provide ferritic stainless steel sheets.
[0008]
BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in more detail.
I do.
Cr: Cr is a very effective element for corrosion resistance. Its effect
Since the fruit becomes remarkable at 11 wt% or more, the lower limit is 11 w
t%. Although there is no particular upper limit, 50
Exceeding the weight wt% not only increases the hot strength but also cools
Since ductility also decreases, it becomes difficult to manufacture, so it is preferable
Is preferably 50% by weight or less.
Ti: Ti is a very important element in the present invention.
It is. Control the size and distribution of precipitates as described below
During recrystallization during annealing after cold rolling,
Colonies and bands that cause ridging phenomena that are likely to occur
Contributes to the inhibition of tissue growth. In particular, sulfur
Formation of carbides, carbides and nitrides is effective. In FIG.
6.4 wt% Cr steel (Fe-16.4 wt% Cr-0.
4wt% Si-0.2wt% Mn-0.005wt% C
-0.009 wt% N-0.003 wt% N-0.30
wt% P-0.50wt% Mo)
Effect of Ti / (C + N) on ridging resistance when changed
+ S), but Ti / (C + N + S) is 3 or more
It can be seen that the ridging resistance is remarkably excellent.
[0010] (Carbide + nitride + sulfide
The average grain size of the steel sheet is dmeanWhen
(Dmean)Two One or more per volume
Is 0.5%The following are the core technologies of the present invention.
is there. Precipitates with a particle size of 3 μm or less are recrystallized after cold rolling.
(100) Prevents the formation of colonies and banded tissue
This is because ridging is suppressed. At this time,
The size (particle size) of the product must be 3 μm or less
No. This is effective when recrystallizing beyond 3 μm (10
0) can prevent the formation of colonies and band-like tissue
This is because the effect of the present invention cannot be obtained.
FIG. 2 shows Fe-18.1 wt% Cr-0.4.
wt% Mn-0.009wt% C-0.012wt% N
-0.003wt% S-0.20wt% Ti (carbide
+ Nitride + sulfide) number / (dmean)Two Lysine for
The score was shown. As shown in Fig. 2, improved ridging resistance
In view of the above, the precipitate has an average grain size of dmeanMade
Sometimes (dmean)Two Must be at least one per
No. Below that, the precipitate is effective for improving ridging resistance
Because it does not act on
Further, the amount of these precipitates is 0.1% by volume.5
%Must be: 0.5%Beyond, corrosion resistance
This is because a decrease in the pitting resistance, especially the pitting corrosion resistance, tends to occur.
Here, regarding the precipitates, carbides, nitrides, and sulfides
Meet the requirements of the present invention, whether alone or in combination
If there is no limitation.
[0013] Ferritic stainless steel has corrosion resistance and
Is the purpose of improving various properties such as oxidation resistance and mechanical properties?
Et al., Si, Mn, Al, Mo, Ni, Cu, Nb, V,
Various elements such as W, Ca, Mg, B, P, Ta, Zr
These sources may be added or as unavoidable impurities.
Element, O, As, Bi, Sb, etc. are mixed. Basically a book
If the conditions of the invention are satisfied, the addition of these components or
There is no problem, and there is no limitation.
The ferrite having excellent ridging resistance according to the present invention.
Series stainless steel sheets are generally industrially:
Manufactured by the method. Thickness by continuous casting after melting
Obtains a slab of about 160 to 260 mm. At this time,
The precipitation form (size, distribution) of carbide, nitride, and sulfide
From the point of view, preferably high-speed casting (for example, a casting speed of 0.7 m
/ Min or more). The slab is then hot rolled.
The hot rolled steel strip has a thickness of 1.5 mm to 6 mm.
At this time, the size of the precipitate, which is the point of the present invention,
From the viewpoint of the distribution and the slab soaking temperature, 1200 ° C or less
preferable. In addition, from the viewpoint of fine precipitation of TiC or TiN
The rough rolling end temperature during hot rolling is 1050 ° C to 950 ° C.
Is preferable, and at least one pass in rough rolling is required.
The rolling reduction is preferably 30% or more. Typically
The obtained hot-rolled steel strip is subjected to recrystallization annealing.
Although the temperature varies depending on the amount of alloying elements,
In order to obtain the effect, if it exceeds 1150 ° C,
Precipitated carbon / nitride coarsening or solid solution easily occurs
Therefore, the temperature is preferably 1150 ° C. or lower. What
Note that annealing of the hot-rolled steel strip is not essential,
In addition, the present application is achieved even if cold rolling is performed. As cold rolled steel sheet
When used, further cold rolling and recrystallization annealing
Will be applied. In particular, for the recrystallization annealing, the effect of the present application
From the viewpoint of the precipitate morphology (size and distribution)
0 ° C. or less, and the average crystal grain size
The thickness is preferably 150 μm or less.
[0015]
DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below based on embodiments.
30 kg of various alloys shown in Table 1 were melted experimentally and
Plate thickness 4 by hot rollingmmHot rolled sheet. Obtained
The hot rolled sheet was descaled after recrystallization annealing, and the sheet thickness was 0.7m
mCold-rolled until recrystallization annealing to produce a cold-rolled annealed plate
Was.
Evaluation of the ridging resistance is as follows.
of ridging generated on the surface of steel sheet after applying t% tensile strain
The degree was evaluated. Observation of precipitates was performed by SEM.
The number was measured by observing 00 visual fields. Also, the average crystal grain size
Was determined by a cutting method using an optical microscope. From both,
(Dmean)Two The number of precipitates with a particle size of 3 μm or less per area
I asked. Table 2 shows the evaluation results of the ridging resistance. Example of the present invention
Has excellent ridging resistance in each case
You can see that. On the other hand, the number of precipitates of 3 μm or less is small.
Or if Ti / (C + N + S) is less than 3
It can be seen that the ridging resistance is poor.
[0017]
[Table 1]
[0018]
[Table 2][0019]
According to the present invention, Ti / (C + N + S)
Is not less than 3 and the average grain size is dmeanAnd
At the same time, carbides, sulfides and nitrides with a particle size of 3 μm or less (d
mean) Two Blow by having one or more per
To significantly improve the ridging resistance of stainless steels.
Now you can do it.
【図面の簡単な説明】
【図１】Ｔｉ／（Ｃ＋Ｎ＋Ｓ）とリジング評点との関係
を示すグラフである。
【図２】（炭化物＋窒化物＋硫化物）個数／（ｄmean）
2 とリジング評点との関係を示すグラフである。BRIEF DESCRIPTION OF THE DRAWINGS FIG. 1 is a graph showing the relationship between Ti / (C + N + S) and ridging scores. FIG. 2 (carbide + nitride + sulfide) number / (d mean )
6 is a graph showing the relationship between 2 and ridging scores.
───────────────────────────────────────────────────── フロントページの続き (58)調査した分野(Int.Cl.7，ＤＢ名) C22C 38/00 - 38/60 ──────────────────────────────────────────────────続 き Continued on front page (58) Field surveyed (Int. Cl. 7 , DB name) C22C 38/00-38/60
Claims (1)
イト系ステンレス鋼板において、重量比でＴｉが０．０
９〜０．４１％でかつＴｉ／（Ｃ＋Ｎ＋Ｓ）≧３で、鋼
板の平均結晶粒径をｄmeanとした時に粒径３μｍ以下の
Ｔｉの炭化物、窒化物及び硫化物の析出物が（ｄmean）
2 あたり１個以上存在し、Ｔｉの炭化物、窒化物及び硫
化物の析出物の体積割合が０．５％以下であることを特
徴とする耐リジング性に優れたフェライト系ステンレス
鋼板。(57) [Claims 1] In a ferritic stainless steel sheet containing 11 wt% or more of Cr, the weight ratio of Ti is 0.0
9 to 0.41% and Ti / (C + N + S) ≧ 3, where the average grain size of the steel sheet is d mean and the grain size is 3 μm or less.
Ti carbides , nitrides and sulfide precipitates (d mean )
A ferritic stainless steel sheet excellent in ridging resistance, characterized in that at least one per 2 is present and the volume fraction of carbides , nitrides and sulfides of Ti is 0.5% or less. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03221896A JP3446449B2 (en) | 1996-02-20 | 1996-02-20 | Ferritic stainless steel sheet with excellent ridging resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP03221896A JP3446449B2 (en) | 1996-02-20 | 1996-02-20 | Ferritic stainless steel sheet with excellent ridging resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH09227999A JPH09227999A (en) | 1997-09-02 |
| JP3446449B2 true JP3446449B2 (en) | 2003-09-16 |
Family
ID=12352804
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP03221896A Expired - Lifetime JP3446449B2 (en) | 1996-02-20 | 1996-02-20 | Ferritic stainless steel sheet with excellent ridging resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3446449B2 (en) |
Families Citing this family (13)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5868875A (en) * | 1997-12-19 | 1999-02-09 | Armco Inc | Non-ridging ferritic chromium alloyed steel and method of making |
| US6855213B2 (en) * | 1998-09-15 | 2005-02-15 | Armco Inc. | Non-ridging ferritic chromium alloyed steel |
| TW496903B (en) * | 1997-12-19 | 2002-08-01 | Armco Inc | Non-ridging ferritic chromium alloyed steel |
| US6238455B1 (en) * | 1999-10-22 | 2001-05-29 | Crs Holdings, Inc. | High-strength, titanium-bearing, powder metallurgy stainless steel article with enhanced machinability |
| JP4959061B2 (en) * | 2001-02-26 | 2012-06-20 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet with excellent overhanging property and method for producing the same |
| CN1307320C (en) | 2002-06-17 | 2007-03-28 | 杰富意钢铁株式会社 | Titanium-added ferritic stainless steel sheet and production method therefor |
| CN100507048C (en) * | 2004-01-28 | 2009-07-01 | 日新制钢株式会社 | Ferritic stainless steel for solid polymer fuel cell separator and solid polymer fuel cell |
| JP4508709B2 (en) * | 2004-04-13 | 2010-07-21 | 新日鐵住金ステンレス株式会社 | Highly efficient descaling method for ferritic heat resistant steel sheet |
| EP2460900B1 (en) * | 2009-07-30 | 2015-04-15 | JFE Steel Corporation | Stainless steel for fuel cell separators which has excellent electrical conductivity and ductility, and process for production thereof |
| JP5960951B2 (en) * | 2011-03-30 | 2016-08-02 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet for automobile fuel tank with excellent fatigue characteristics and method for producing the same |
| CN103316929B (en) * | 2012-03-21 | 2015-03-04 | 宝山钢铁股份有限公司 | Rolling and cooling technology method for reducing GCR15 bearing steel zonary carbide level |
| UA111115C2 (en) * | 2012-04-02 | 2016-03-25 | Ейкей Стіл Пропертіс, Інк. | cost effective ferritic stainless steel |
| CN106232838A (en) * | 2013-12-24 | 2016-12-14 | Posco公司 | Ferritic stainless steel that mouldability and wrinkle resistance are improved and manufacture method thereof |
-
1996
- 1996-02-20 JP JP03221896A patent/JP3446449B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH09227999A (en) | 1997-09-02 |
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