JP3608636B2 - Ferritic stainless steel with excellent workability - Google Patents
Ferritic stainless steel with excellent workability Download PDFInfo
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- JP3608636B2 JP3608636B2 JP09730296A JP9730296A JP3608636B2 JP 3608636 B2 JP3608636 B2 JP 3608636B2 JP 09730296 A JP09730296 A JP 09730296A JP 9730296 A JP9730296 A JP 9730296A JP 3608636 B2 JP3608636 B2 JP 3608636B2
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- 229910001220 stainless steel Inorganic materials 0.000 title claims description 14
- 239000002244 precipitate Substances 0.000 claims description 20
- 238000000137 annealing Methods 0.000 claims description 9
- 229910052804 chromium Inorganic materials 0.000 claims description 2
- 229910052748 manganese Inorganic materials 0.000 claims description 2
- 239000012535 impurity Substances 0.000 claims 1
- 238000001953 recrystallisation Methods 0.000 description 20
- 229910000831 Steel Inorganic materials 0.000 description 15
- 239000010959 steel Substances 0.000 description 15
- 229910052758 niobium Inorganic materials 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 238000005098 hot rolling Methods 0.000 description 6
- 239000000126 substance Substances 0.000 description 5
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 3
- 150000001247 metal acetylides Chemical class 0.000 description 3
- 150000004767 nitrides Chemical class 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000005336 cracking Methods 0.000 description 2
- 230000003111 delayed effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000002708 enhancing effect Effects 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- -1 TiC or Nb (C Chemical class 0.000 description 1
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 238000005256 carbonitriding Methods 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000003792 electrolyte Substances 0.000 description 1
- 238000000866 electrolytic etching Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000011084 recovery Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 239000002904 solvent Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- 238000004804 winding Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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Description
【０００１】
【発明の属する技術分野】
本発明は加工性に優れたフェライト系ステンレス鋼に関するものである。
【０００２】
【従来の技術】
ステンレス鋼は、ＳＵＳ４３０に代表されるフェライト系ステンレス鋼と、ＳＵＳ３０４に代表されるオーステナイト系ステンレス鋼に大別される。フェライト系ステンレス鋼はオーステナイト系ステンレス鋼に比べて成形後に時期割れ現象がなく、応力腐食割れ感受性が小さく、熱膨張係数が小さい等の特徴を有し、また高価なＮｉを含有せず廉価であることから、建築用材料、厨房用材料及び電気部品用材料などとして多用されている。
【０００３】
しかしながら、フェライト系ステンレス鋼はオーステナイト系ステンレス鋼に比べて溶接性、プレス加工性などの材料特性が一般的に劣るので、用途が限定される面もある。特にステンレス鋼は、プレス加工によって最終製品に加工される場合が多いので、プレス加工性（以後、単に加工性と呼ぶ）は重要な材料特性の一つである。
【０００４】
そこで、フェライト系ステンレス鋼の加工性向上を目的として数多くの鋼が開発されている。例えば、特開昭５１−１４８１１号、特開昭５１−１４８１２号及び特開昭５２−３１９１９号などがある。これらはＣ及びＮの低減と比較的多量のＴｉやＮｂなどの炭窒化物形成元素の添加を組み合わせて、加工性の改善を図っている。
【０００５】
【発明が解決しようとする課題】
上述したようなＴｉあるいはＮｂの添加により、加工性の向上が図れるものの、再結晶温度が上昇するため製造コストが高くなる。また熱間圧延時に形成された圧延方向に長く伸びた展伸粒が完全には再結晶せず、焼鈍後にも残留し、加工性が低下するという問題がある。このため、特開昭５４−７９１１７号などに示されている熱間圧延の低温巻取や特公昭６１−５１０１２号などに示されている熱間圧延の低温仕上げなどにより、熱間圧延後に歪みの蓄積を図り、再結晶特性を改善する方法や特開昭５４−１１４４２２号に示されている熱間圧延時に異径ロールを用いることにより、熱延時の歪みをより内部まで導入して再結晶特性の改善を図る方法などがなされている。しかしながら、これらの方法によっても必ずしも十分な再結晶特性の改善は困難であり、未だ展伸粒が残存して良好な加工性が得られないという問題がある。
【０００６】
本発明は上記の問題点を鑑みてなされたもので、Ｃ、Ｎ、Ｔｉ及びＮｂなどの化学成分と鋼中の１μｍ以下の大きさの析出物数を規定する事によって再結晶特性を改善し、加工性に優れたフェライト系ステンレス鋼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】
一般に金属材料においては、その材料中に存在する炭化物、窒化物などの析出物は転位及びサブバウンダリーをピン止めして、回復あるいは再結晶を遅滞させると考えられている。本発明者らは、上記課題の解決に当たり、再結晶特性及び加工性に及ぼす析出物の影響について詳細に検討した結果、１μｍ以下の大きさのＴｉＣあるいはＮｂ（Ｃ，Ｎ）といった炭化物あるいは炭窒化物などの析出物が再結晶を遅滞させ、再結晶特性の改善には、それらの析出物量の低下が有効であるとの知見を得た。本発明では、Ｃ、Ｎの低減と１μｍ以下の大きさの析出物数を規定することにより、再結晶を促進し良好な加工性を得ることができる。
【０００８】
本発明は、上記の知見に基づいてなされたものである。すなわち、本発明の要旨は、ｍａｓｓ％でＣ：０．０２％以下、Ｓｉ：１．０％以下、Ｍｎ：１．０％以下、Ｃｒ：１０〜３５％、Ｎ：０．０２％以下を含有し、さらに、Ｔｉ：Ｔｉ／（Ｃ＋Ｎ）が４以上〜０．３０％、及びＮｂ：Ｎｂ／（Ｃ＋Ｎ）が７以上〜０．５０％の１種または２種を含有し、残部がＦｅ及び不可避的に混入する不純物とからなり、熱延板焼鈍時の１μｍ以下の大きさの析出物数が１００μｍ２あたり１００個以下であることを特徴とする。
【０００９】
【発明の実施の形態】
以下に本発明の成分範囲を限定した理由を述べる。
Ｃ、Ｎ：一般にフェライト系ステンレス鋼にとって、Ｃ、ＮはＣｒを粒界に炭窒化物として析出させ、耐粒界腐食性と靭性を悪くさせること、及びＴｉあるいはＮｂと結合して再結晶を遅滞させる微細な炭化物、窒化物を生成するため、低く押さえることが好ましいので、それぞれ０．０２％以下とした。
【００１０】
Ｓｉ：Ｓｉは脱酸剤であり、耐酸化性を高めるのに有効であるが、多量に含有すると材料が硬化し、加工性に悪影響を与えるようになるので、１．０％以下とした。
【００１１】
Ｍｎ：Ｍｎは熱間加工性や溶接部の靭性を改善する元素であるが、多量に含有すると加工性に影響を与えるので、１．０％以下とした。
【００１２】
Ｃｒ：Ｃｒは鋼の耐食性、耐高温酸化性などの特性を高めるのに有益な元素であり、最低限の特性を確保するためには１０％以上の含有量を確保する必要がある。一方、３５％を越えて含有させると、素材の靭性や成形性の低下が著しくなる。このためにＣｒは１０〜３５％とした。
【００１３】
Ｔｉ、Ｎｂ：Ｔｉ、Ｎｂは鋼中のＣ、ＮをＴｉＣ、ＴｉＮ、Ｎｂ（Ｃ，Ｎ）として固定する炭化物、窒化物、炭窒化物形成元素である。Ｃ、Ｎの固定のためには最低限Ｔｉ／（Ｃ＋Ｎ）を４以上、Ｎｂ／（Ｃ＋Ｎ）を７以上とする必要がある。また、Ｔｉ、Ｎｂの絶対量を過剰に添加することは鋼の表面性状の劣化や固溶Ｔｉ、Ｎｂ量の増加による靭性の劣化及びコスト上昇を招くので、Ｔｉについては０．３０％、Ｎｂについては０．５０％を上限とした。
【００１４】
なお、耐食性向上のため３．０％以下のＭｏ、１．０％以下のＣｕを、耐酸化性の向上のために１．０％以下のＡｌを、炭窒化物形成による加工性向上のために０．５％以下のＺｒ、Ｖを、熱間加工性向上のために０．０５％以下のＢ、ＲＥＭを添加しても良い。
【００１５】
【実施例】
以下の実施例をもとに、１μｍ以下の大きさの析出物数を限定した理由を示す。
表１に示した化学成分のフェライト系ステンレス鋼を５０ｋｇ真空溶解炉にて溶解した。これを表２に示すように１１５０〜１２５０℃に加熱・均熱後、仕上温度８００〜８５０℃で板厚３０ｍｍから３．６ｍｍまで熱間圧延した。その後熱延板焼鈍を８５０〜１２００℃で行い、熱延板焼鈍板のＬ断面の金属組織を観察して、熱延板の再結晶温度を調べた。熱延板をその再結晶温度で焼鈍を行った後、酸洗し、板圧０．７ｍｍまで冷延した。冷延板についても表２に示すように８００〜１１００℃の焼鈍を行い、冷延板の再結晶温度を調べ、その再結晶温度で焼鈍を行ったものを供試材とした。なお、表１では本発明例としてＮｏ．１及び２の鋼はＣ、Ｎを低減し、ＴｉをＴｉ／（Ｃ＋Ｎ）で５〜９の範囲で変動させた鋼であり、Ｎｏ．３〜５はＣ、Ｎを低減し、ＮｂをＮｂ／（Ｃ＋Ｎ）で１０〜３４の範囲で変動させた鋼である。また、比較例としてＮｏ．６及び７の鋼はＣ、Ｎを低減し、ＴｉをＴｉ／（Ｃ＋Ｎ）で１３〜３１の範囲で変動させた鋼であり、Ｎｏ．８及び９はＣ、Ｎを低減し、Ｎｂを１４〜２１の範囲で変動させた鋼である。
【００１６】
上記工程により得られた供試材について、ＪＩＳ１３Ｂ号試験片を用いて、伸び及び加工性特に深絞り性の指標となるｒ値を求めた。また、それぞれの材料において熱延板焼鈍後の析出物数が最大となる温度で熱延板焼鈍を施した後、熱延板焼鈍板のＬ断面について、非水溶媒系電解液を用いた定電位電解エッチング法により、マトリックスのみを溶解し析出物を残存させた後、倍率６０００倍で２５μｍ２の範囲に観察される１μｍ以下の大きさの析出物数をカウントした。
【００１７】
１μｍ以下の大きさの析出物数：図１は本発明の化学組成範囲にあるフェライト系ステンレス鋼について、１００μｍ２あたりの１μｍ以下の大きさの析出物数
と熱延板焼鈍時に展伸粒が完全に消失する再結晶温度の関係を示したものである。
図１によると、１００μｍ２あたり１００個を超える範囲で再結晶温度が顕著に上昇している。したがって、再結晶温度を改善し加工性を向上させるためには、１μｍ以下の大きさの析出物数が１００μｍ２あたり１００個以下とする必要がある。
【００１８】
表１の結果から明らかなように、本発明で規定する化学成分範囲であり、かつ１μｍ以下の大きさの析出物数が１００μｍ２あたり１００個以下であるＮｏ．１〜５の鋼は伸びが３５．２％以上で、ｒ値が１．７１以上であり加工性が良好である。一方、本発明で規定する化学成分範囲であるが、１μｍ以下の大きさの析出物数が１００μｍ２あたり１００個より多いＮＯ．６、８および９の鋼、及び本発明で規定する化学成分範囲外であるＮｏ．７の鋼は伸びが３０．５％以下で、ｒ値が１．６７以下であり、上記Ｎｏ．１〜５の鋼に比べて加工性が劣っている。
【００１９】
【表１】
【表２】
【発明の効果】
本発明によれば、次の効果が生まれる。
（１） 従来のＴｉ、Ｎｂを含み低Ｃ、Ｎ化したフェライト系ステンレス鋼より
も高い加工性を有する鋼を得ることができる。
（２） 再結晶温度が低下するので、焼鈍時の炉温の低下あるいはラインスピー
ドのアップによるコストダウンが期待できる。
【図面の簡単な説明】
【図１】熱延板焼鈍時の大きさ１μｍ以下の析出物の１００μｍ２当たりの析出物数と再結晶温度の関係を示す図である。[0001]
BACKGROUND OF THE INVENTION
The present invention relates to a ferritic stainless steel excellent in workability.
[0002]
[Prior art]
Stainless steel is roughly classified into ferritic stainless steel represented by SUS430 and austenitic stainless steel represented by SUS304. Compared to austenitic stainless steel, ferritic stainless steel has features such as no cracking after molding, low stress corrosion cracking susceptibility, low thermal expansion coefficient, etc., and it is inexpensive and does not contain expensive Ni. For this reason, it is frequently used as a building material, a kitchen material, an electrical component material, and the like.
[0003]
However, ferritic stainless steel is generally inferior in material properties such as weldability and press workability as compared to austenitic stainless steel, and therefore has limited applications. In particular, since stainless steel is often processed into a final product by pressing, press workability (hereinafter simply referred to as workability) is one of important material properties.
[0004]
Therefore, many steels have been developed for the purpose of improving the workability of ferritic stainless steel. For example, there are JP-A-51-14811, JP-A-51-14812, and JP-A-52-31919. These are intended to improve workability by combining the reduction of C and N with the addition of relatively large amounts of carbonitride-forming elements such as Ti and Nb.
[0005]
[Problems to be solved by the invention]
Although the workability can be improved by adding Ti or Nb as described above, the recrystallization temperature rises, resulting in an increase in manufacturing cost. In addition, there is a problem that the stretched grains elongated in the rolling direction formed at the time of hot rolling are not completely recrystallized and remain even after annealing, thereby reducing workability. For this reason, distortion after hot rolling is caused by low-temperature winding of hot rolling shown in JP-A-54-79117 or low-temperature finishing of hot rolling shown in JP-B 61-51012. Is used to improve the recrystallization characteristics, and by using different diameter rolls during hot rolling as disclosed in JP-A No. 54-114422, the strain at the time of hot rolling is further introduced into the interior for recrystallization. There are methods to improve the characteristics. However, even with these methods, it is not always possible to sufficiently improve the recrystallization characteristics, and there is still a problem that expanded grains remain and good workability cannot be obtained.
[0006]
The present invention has been made in view of the above-mentioned problems, and improves the recrystallization characteristics by defining the chemical components such as C, N, Ti and Nb and the number of precipitates having a size of 1 μm or less in the steel. An object of the present invention is to provide a ferritic stainless steel having excellent workability.
[0007]
[Means for Solving the Problems]
In general, in metal materials, it is considered that precipitates such as carbides and nitrides present in the materials pin the dislocations and subboundaries to delay recovery or recrystallization. In solving the above problems, the present inventors have studied in detail the influence of precipitates on recrystallization characteristics and workability. As a result, carbides such as TiC or Nb (C, N) having a size of 1 μm or less, or carbonitriding. It was found that precipitates such as deposits delayed recrystallization, and that the reduction of the amount of these precipitates was effective in improving the recrystallization characteristics. In the present invention, by specifying the reduction of C and N and the number of precipitates having a size of 1 μm or less, recrystallization can be promoted and good workability can be obtained.
[0008]
The present invention has been made based on the above findings. That is, the gist of the present invention is that mass% is C: 0.02% or less, Si: 1.0% or less, Mn: 1.0% or less, Cr: 10 to 35%, N: 0.02% or less. And Ti: Ti / (C + N) is 4 or more and 0.30%, and Nb: Nb / (C + N) is 7 or more and 0.50%, or the balance is Fe. And the number of precipitates having a size of 1 μm or less at the time of hot-rolled sheet annealing is 100 or less per 100 μm 2 .
[0009]
DETAILED DESCRIPTION OF THE INVENTION
The reason for limiting the component range of the present invention will be described below.
C, N: Generally, for ferritic stainless steel, C and N precipitate Cr as a carbonitride at the grain boundary, deteriorate intergranular corrosion resistance and toughness, and combine with Ti or Nb for recrystallization. In order to produce fine carbides and nitrides that are delayed, it is preferable to keep them low, so each was made 0.02% or less.
[0010]
Si: Si is a deoxidizer and is effective in enhancing oxidation resistance. However, if contained in a large amount, the material is hardened and adversely affects workability.
[0011]
Mn: Mn is an element that improves the hot workability and the toughness of the welded portion, but if contained in a large amount, the workability is affected.
[0012]
Cr: Cr is an element useful for enhancing the properties of steel such as corrosion resistance and high-temperature oxidation resistance, and it is necessary to ensure a content of 10% or more in order to ensure minimum properties. On the other hand, if the content exceeds 35%, the toughness and moldability of the material are significantly lowered. For this reason, Cr was made into 10 to 35%.
[0013]
Ti, Nb: Ti and Nb are carbide, nitride, and carbonitride forming elements that fix C and N in steel as TiC, TiN, and Nb (C, N). In order to fix C and N, at least Ti / (C + N) needs to be 4 or more and Nb / (C + N) needs to be 7 or more. Further, excessive addition of absolute amounts of Ti and Nb leads to deterioration of the surface properties of steel, deterioration of toughness due to an increase in the amount of dissolved Ti and Nb, and cost increase. Therefore, about 0.30% for Ti, Nb About 0.50% was made the upper limit.
[0014]
For improving corrosion resistance, 3.0% or less of Mo, 1.0% or less of Cu, for improving oxidation resistance, 1.0% or less of Al, for improving workability by forming carbonitride In addition, 0.5% or less of Zr and V may be added, and 0.05% or less of B and REM may be added to improve hot workability.
[0015]
【Example】
The reason why the number of precipitates having a size of 1 μm or less is limited based on the following examples will be described.
Ferritic stainless steel having chemical components shown in Table 1 was melted in a 50 kg vacuum melting furnace. As shown in Table 2, this was heated to 1150 to 1250 ° C. and soaked, and then hot-rolled from a sheet thickness of 30 mm to 3.6 mm at a finishing temperature of 800 to 850 ° C. Thereafter, hot-rolled sheet annealing was performed at 850 to 1200 ° C., and the metal structure of the L cross section of the hot-rolled sheet annealed sheet was observed to examine the recrystallization temperature of the hot-rolled sheet. The hot-rolled sheet was annealed at the recrystallization temperature, then pickled and cold-rolled to a sheet pressure of 0.7 mm. As shown in Table 2, the cold-rolled sheet was annealed at 800 to 1100 ° C., the recrystallization temperature of the cold-rolled sheet was examined, and the sample annealed at the recrystallization temperature was used as a test material. In Table 1, as an example of the present invention, No. Steels Nos. 1 and 2 are steels in which C and N are reduced and Ti is changed in a range of 5 to 9 with Ti / (C + N). 3 to 5 are steels in which C and N are reduced and Nb is varied in a range of 10 to 34 by Nb / (C + N). As a comparative example, No. Steels Nos. 6 and 7 are steels in which C and N are reduced and Ti is changed in a range of 13 to 31 with Ti / (C + N). 8 and 9 are steels in which C and N are reduced and Nb is varied in the range of 14-21.
[0016]
About the test material obtained by the said process, r value used as a parameter | index of elongation and workability especially deep drawability was calculated | required using the JIS13B test piece. Moreover, after performing hot-rolled sheet annealing at a temperature at which the number of precipitates after hot-rolled sheet annealing is maximized in each material, the L cross-section of the hot-rolled sheet annealed sheet is determined using a nonaqueous solvent electrolyte. After dissolving only the matrix and leaving the precipitates by the potential electroetching method, the number of precipitates having a size of 1 μm or less observed in a range of 25 μm 2 at a magnification of 6000 was counted.
[0017]
Number of precipitates having a size of 1 μm or less: FIG. 1 shows the number of precipitates having a size of 1 μm or less per 100 μm 2 in the ferritic stainless steel in the chemical composition range of the present invention and the number of stretched grains during hot-rolled sheet annealing The relationship of the recrystallization temperature which lose | disappears completely is shown.
According to FIG. 1, the recrystallization temperature rises remarkably in the range exceeding 100 per 100 μm 2 . Therefore, in order to improve the recrystallization temperature and improve the workability, the number of precipitates having a size of 1 μm or less needs to be 100 or less per 100 μm 2 .
[0018]
As is apparent from the results in Table 1, No. 1 is a chemical component range defined in the present invention, and the number of precipitates having a size of 1 μm or less is 100 or less per 100 μm 2 . Steels 1 to 5 have an elongation of 35.2% or more, an r value of 1.71 or more, and good workability. On the other hand, in the chemical component range defined in the present invention, the number of precipitates having a size of 1 μm or less is more than 100 per 100 μm 2 . Steels Nos. 6, 8 and 9 and Nos. No. 7 has an elongation of 30.5% or less and an r value of 1.67 or less. Workability is inferior compared to 1-5 steel.
[0019]
[Table 1]
[Table 2]
【The invention's effect】
According to the present invention, the following effects are produced.
(1) Steel having higher workability than conventional ferritic stainless steel containing Ti and Nb and having low C and N content can be obtained.
(2) Since the recrystallization temperature is lowered, it can be expected that the furnace temperature during annealing is lowered or the cost is reduced by increasing the line speed.
[Brief description of the drawings]
FIG. 1 is a graph showing the relationship between the number of precipitates per 100 μm 2 and the recrystallization temperature of precipitates having a size of 1 μm or less during hot-rolled sheet annealing.
Claims (1)
Ｔｉ／（Ｃ＋Ｎ）が４以上かつＴｉ：０．３０重量％以下及びＮｂ／（Ｃ＋Ｎ）が７以上かつＮｂ：０．５０重量％以下を１種または２種を含有し、残部がＦｅ及び不可避的に混入する不純物とからなり、熱延板焼鈍時の１μｍ以下の析出物数が１００μｍ２あたり１００個以下であることを特徴とする加工性に優れたフェライト系ステンレス鋼。C: 0.02 wt% or less, Si: 1.0 wt% or less, Mn: 1.0 wt% or less, Cr: 10 to 35 wt%, N: 0.02 wt% or less, and Ti / (C + N) is 4 or more and Ti: 0.30% by weight or less and Nb / (C + N) is 7 or more and Nb: 0.50% by weight or less, containing one or two kinds, the balance being Fe and inevitable A ferritic stainless steel excellent in workability, comprising impurities mixed therein, wherein the number of precipitates of 1 μm or less during hot-rolled sheet annealing is 100 or less per 100 μm 2 .
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|---|---|---|---|
| JP09730296A JP3608636B2 (en) | 1996-03-28 | 1996-03-28 | Ferritic stainless steel with excellent workability |
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| JP09730296A JP3608636B2 (en) | 1996-03-28 | 1996-03-28 | Ferritic stainless steel with excellent workability |
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| JPH09263903A JPH09263903A (en) | 1997-10-07 |
| JP3608636B2 true JP3608636B2 (en) | 2005-01-12 |
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| US6651020B2 (en) | 1997-12-24 | 2003-11-18 | Edward S. More | Method and apparatus for economical drift compensation in high resolution measurements |
| KR100473497B1 (en) | 2000-06-20 | 2005-03-09 | 제이에프이 스틸 가부시키가이샤 | Thin steel sheet and method for production thereof |
| JP7688985B2 (en) * | 2021-03-01 | 2025-06-05 | 日鉄ステンレス株式会社 | Ferritic stainless steel material and its manufacturing method, welded member and its manufacturing method, and vibration damping member |
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