JP2000001757A - Ferritic stainless steel good in surface property and excellent in corrosion resistance, forming workability and ridging resistance - Google Patents
Ferritic stainless steel good in surface property and excellent in corrosion resistance, forming workability and ridging resistanceInfo
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- JP2000001757A JP2000001757A JP17187998A JP17187998A JP2000001757A JP 2000001757 A JP2000001757 A JP 2000001757A JP 17187998 A JP17187998 A JP 17187998A JP 17187998 A JP17187998 A JP 17187998A JP 2000001757 A JP2000001757 A JP 2000001757A
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- oxide
- less
- steel
- corrosion resistance
- stainless steel
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、鋼板表面性状が
良好で、耐食性と成形加工性および耐リジング性に優れ
たフェライト系ステンレス鋼に関し、とくに鋼中に含ま
れる酸化物系介在物の組成を改質することによって諸特
性の有利な改善を図ったものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a ferritic stainless steel having good surface properties of a steel sheet and excellent corrosion resistance, formability and ridging resistance, and particularly to a composition of oxide inclusions contained in the steel. By reforming, various properties are advantageously improved.
【０００２】[0002]
【従来の技術】フェライト系ステンレス鋼板は、主要合
金元素としてNiを含まず、安価であるため、自動車用部
品や電機・厨房機器関連分野をはじめとして幅広く使用
されている。2. Description of the Related Art Ferritic stainless steel sheets do not contain Ni as a main alloying element and are inexpensive. Therefore, they are widely used in automobile parts, electric and kitchen equipment-related fields.
【０００３】例えば、特開昭61−276955号公報には、
Ｃ，Ｎの低減とTi添加によって深絞り成形加工性の指標
であるｒ値を向上させ、さらにＢ添加によって深絞り加
工後の２次加工脆性を改善する技術が開示されている。
この技術では、Alを積極的に添加することによって、Ti
O2の生成を抑制し、鋼板表面に欠陥が発生することを防
止している。しかしながら、この技術では、得られる表
面品質が十分満足するまでには至らないだけでなく、製
造時の連続鋳造時に、浸漬ノズルの内壁に Al2O3−TiO2
系の高融点介在物が付着堆積し、ノズル閉塞が生じるい
う問題があった。[0003] For example, JP-A-61-276955 discloses that
There is disclosed a technique for improving the r-value, which is an index of deep drawing formability, by reducing C and N and adding Ti, and further improving the brittleness of secondary working after deep drawing by adding B.
In this technology, by actively adding Al, Ti
The generation of O 2 is suppressed, and the occurrence of defects on the steel sheet surface is prevented. However, in this technique, not only the obtained surface quality is not sufficiently satisfied, but also during the continuous casting at the time of manufacturing, the inner wall of the immersion nozzle is Al 2 O 3 -TiO 2
There was a problem that the high melting point inclusions of the system adhered and deposited, causing nozzle clogging.
【０００４】また、特開平８−144021号公報や特開平８
−260106号公報には、Alを含有したTi添加フェライト系
ステンレス鋼において、上述した連続鋳造時におけるノ
ズル閉塞対策として、酸化物系介在物を Al2O3−TiO2−
CaO 系とし、低融点化することによって、ノズル詰まり
を防止する技術が開示されている。しかしながら、この
技術では、介在物としてCaＳが生成し易く、このCaＳが
起点となって錆が発生し易いため、耐食性が劣化すると
いう問題があり、低Ｓ化が必要となる。しかも、基本的
にAl脱酸技術であるため、冷延板において、 Al2O3が凝
集、クラスター化して発生するヘゲ状の表面欠陥が免れ
得ないという根本的な問題を残していた。Further, Japanese Patent Application Laid-Open Nos.
-260106 discloses that, in a Ti-added ferritic stainless steel containing Al, as a measure against nozzle clogging at the time of the above-described continuous casting, an oxide-based inclusion is made of Al 2 O 3 —TiO 2 −
There is disclosed a technique of preventing nozzle clogging by using a CaO-based material and lowering the melting point. However, in this technique, CaS is easily generated as an inclusion, and rust is easily generated from the CaS as a starting point. Therefore, there is a problem that corrosion resistance is deteriorated, and a low S is required. Moreover, since it is basically an Al deoxidation technique, there remains a fundamental problem that in the cold rolled sheet, barbed surface defects generated by agglomeration and clustering of Al 2 O 3 cannot be avoided.
【０００５】一方、フェライト系ステンレス鋼は、加工
時に圧延方向に沿ってリジングと呼ばれる「しわ」が表
面に発生し易く、ステンレス鋼板本来の美観を損なうば
かりか、リジングを除去するために、加工後に研磨工程
が必要になるという問題がある。この問題の改善策とし
ては、従来、熱間圧延時の粗圧延１パスあたりの圧下量
を増やしたり、あるいは仕上げ圧延スケジュールを最適
化することが行われてきたが、このような方法では、熱
延時に表面に疵が入り易いだけでなく、大量生産を安定
して実施することが難しいという問題があった。On the other hand, ferritic stainless steel tends to have wrinkles, called ridging, on the surface along the rolling direction during processing, which not only impairs the original appearance of the stainless steel plate, but also removes ridging after processing. There is a problem that a polishing step is required. In order to solve this problem, conventionally, the rolling reduction per pass of the rough rolling in hot rolling has been increased, or the finish rolling schedule has been optimized. There is a problem that not only is the surface easily damaged during rolling, but it is difficult to stably perform mass production.
【０００６】[0006]
【発明が解決しようとする課題】この発明は、上記の実
情に鑑み開発されたもので、上述したような従来の問題
を全て解決した、表面性状が良好で耐食性、成形加工性
および耐リジング性に優れたフェライト系ステンレス鋼
を提案することを目的とする。すなわち、この発明にお
ける課題は次のとおりである。 (1) 製造時の連続鋳造時にノズル詰まりが無く、製造性
がよいこと。 (2) ヘゲ状表面欠陥がなく表面性状に優れること。 (3) 耐食性に優れること。 (4) 成型加工性に優れること。具体的には、ｒ値が 1.7
以上でΔｒ値が 0.2以下であること。 (5) 成形加工部でリジング発生程度が軽微であること。DISCLOSURE OF THE INVENTION The present invention has been developed in view of the above-mentioned circumstances, and solves all of the above-mentioned conventional problems. It has good surface properties, corrosion resistance, moldability and ridging resistance. It is intended to propose a ferritic stainless steel excellent in quality. That is, the subject in this invention is as follows. (1) No nozzle clogging during continuous casting during production and good productivity. (2) Excellent surface properties without barbed surface defects. (3) Excellent corrosion resistance. (4) Excellent moldability. Specifically, the r value is 1.7
Above, the Δr value should be 0.2 or less. (5) The degree of ridging generated in the molded part should be minimal.
【０００７】[0007]
【課題を解決するための手段】さて、発明者らは、上記
の目的を達成すべく、鋭意研究を重ねた結果、鋼材の成
分調整もさることながら、鋼中に含まれる酸化物系介在
物の組成を適正に改質することが、所期した目的の達成
に関し極めて有効であること、また酸化物系介在物を所
望組成に安定して改質するには、鋼成分のうち脱酸剤と
して作用する成分の添加順序が極めて重要であることの
知見を得た。この発明は、上記の知見に立脚するもので
ある。Means for Solving the Problems The inventors of the present invention have conducted intensive studies in order to achieve the above-mentioned object, and have found that the oxide-based inclusions contained in the steel can be adjusted while controlling the composition of the steel material. It is extremely effective to appropriately modify the composition of the steel to achieve the intended purpose. To stably modify the oxide-based inclusions to the desired composition, a deoxidizing agent must be used among the steel components. It has been found that the order of addition of the components acting as a material is extremely important. The present invention is based on the above findings.
【０００８】すなわち、この発明の要旨構成は次のとお
りである。 １．Ｃ：0.02wt％以下、 Si：1.0 wt％以下、 Mn：1.0 wt％以下、 Cr：５〜50wt％、 Ｐ：0.05wt％以下、 Ｓ：0.015 wt％以下、 Ｎ：0.02wt％以下、 Al：0.005 wt％以下、 Ｏ：0.01wt％以下、 Ti：0.08wt％以上かつ６×（Ｃ＋Ｎ）以上、0.5 wt％以下、 （Ｖ＋Nb）：0.04〜0.1 wt％でかつＶ／Nb＝2.0 〜5.0 、 Ca：0.0005〜0.0050wt％ を含有し、残部は実質的にFeの組成になり、鋼中の脱酸
生成物に起因した酸化物系介在物の組成が、Ti酸化物：
20〜90wt％、 Al2O3：50wt％以下およびCaＯ：５〜50wt
％の範囲を満足することを特徴とする表面性状が良好で
耐食性、成形加工性および耐リジング性に優れたフェラ
イト系ステンレス鋼。That is, the gist configuration of the present invention is as follows. 1. C: 0.02 wt% or less, Si: 1.0 wt% or less, Mn: 1.0 wt% or less, Cr: 5 to 50 wt%, P: 0.05 wt% or less, S: 0.015 wt% or less, N: 0.02 wt% or less, Al : 0.005 wt% or less, O: 0.01 wt% or less, Ti: 0.08 wt% or more and 6 × (C + N) or more, 0.5 wt% or less, (V + Nb): 0.04 to 0.1 wt% and V / Nb = 2.0 to 5.0 , Ca: 0.0005 to 0.0050 wt%, the balance being substantially Fe, and the composition of oxide-based inclusions due to deoxidation products in steel is Ti oxide:
20~90wt%, Al 2 O 3: 50wt% or less, and CaO: 5-50 wt
% Ferritic stainless steel with good surface properties and excellent corrosion resistance, moldability and ridging resistance.
【０００９】２．上記１において、鋼組成が、さらに Mo：0.05〜4.0 wt％ を含有する組成になることを特徴とする表面性状が良好
で耐食性、成形加工性および耐リジング性に優れたフェ
ライト系ステンレス鋼。[0009] 2. 1. The ferritic stainless steel according to 1 above, wherein the steel composition further comprises Mo: 0.05 to 4.0 wt%, and the ferrite stainless steel has good surface properties and excellent corrosion resistance, moldability and ridging resistance.
【００１０】３．上記１または２において、鋼組成が、
さらに Ｂ：0.0002〜0.0030wt％ を含有する組成になることを特徴とする表面性状が良好
で耐食性、成形加工性および耐リジング性に優れたフェ
ライト系ステンレス鋼板。[0010] 3. In the above 1 or 2, the steel composition is
Further, B: a ferritic stainless steel sheet which has a composition containing 0.0002 to 0.0030 wt% and has excellent surface properties and excellent corrosion resistance, moldability and ridging resistance.
【００１１】[0011]
【発明の実施の形態】以下、この発明の基礎となった実
験結果について説明する。実験１ Ｃ：0.006 〜0.011 wt％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.003 〜0.011 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、N
b＋Ｖ：0.046〜0.093 wt％でかつＶ／Nb＝2.1 〜4.6 、
Ca：0.0006〜0.0022wt％の成分範囲で、Al量を0.0007wt
％から 0.023wt％まで変化させた鋼を、溶製し、連続鋳
造後（鋳片サイズ：200mm 厚×1240mm幅）、鋳片を手入
れすることなく熱間圧延した。熱間圧延は、スラブ加熱
条件：1090〜1130℃−40〜60分、粗圧延７パス、粗圧延
仕上げ温度：940 〜1000 ℃、粗圧延仕上げ厚：28mm、
仕上げ（７スタンド）圧延機出側温度：800 〜880 ℃、
仕上げ厚：３mm、コイル巻き取り温度：610 ℃、の条件
で行った。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Hereinafter, experimental results on which the present invention is based will be described. Experiment 1 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.003 to 0.011 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, N
b + V: 0.046 to 0.093 wt% and V / Nb = 2.1 to 4.6,
Ca: 0.0006wt to 0.0022wt% component range, Al content 0.0007wt
% Was changed to 0.023 wt%, and the steel was melted and continuously cast (slab size: 200 mm thickness x 1240 mm width), and then hot rolled without care of the slab. For hot rolling, slab heating conditions: 1090 to 1130 ° C-40 to 60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 940 to 1000 ° C, rough rolling finished thickness: 28 mm,
Finishing (7 stands) Rolling mill outlet temperature: 800-880 ° C,
The finishing was carried out under the conditions of a thickness of 3 mm and a coil winding temperature of 610 ° C.
【００１２】ついで、熱延コイルを 880〜920 ℃で連続
焼鈍したのち、酸洗を施してから、コイル全長にわたっ
て表面観察を行い、ヘゲ状欠陥の単位面積当たりの平均
個数を求めた。得られた結果を図１に示す。なお、観察
されたヘゲ状欠陥はいずれも幅が 0.4〜3.0 mm程度で長
さは30〜500 mm程度であった。図１から明らかなよう
に、Al量が 0.005wt％を超えるとヘゲ状欠陥が発生し始
めるのが判る。これらのヘゲ状欠陥部を分析したところ
Al2O3が検出された。従って、かようなヘゲ状欠陥は、
鋳込み時に生成した脱酸生成物である Al2O3が凝集・粗
大化し、熱延時に圧延方向に分断されてできたものと考
えられる。Next, the hot-rolled coil was continuously annealed at 880 to 920 ° C., and after pickling, the surface was observed over the entire length of the coil to determine the average number of barge-shaped defects per unit area. The results obtained are shown in FIG. In addition, each of the observed barbed defects had a width of about 0.4 to 3.0 mm and a length of about 30 to 500 mm. As is clear from FIG. 1, it can be seen that barge-like defects begin to occur when the Al content exceeds 0.005 wt%. Analysis of these barbed defects
Al 2 O 3 was detected. Therefore, such barbed defects are:
It is considered that Al 2 O 3, which is a deoxidation product generated at the time of casting, was agglomerated and coarsened, and was cut off in the rolling direction during hot rolling.
【００１３】実験２ Ｃ：0.006 〜0.011 wt％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.003 〜0.011 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、N
b＋Ｖ：0.046〜0.093 wt％でかつＶ／Nb＝2.1 〜4.6 、
Ca量：0.00090.0024wt％の成分範囲で、Al量を0.0007wt
％から 0.023wt％まで変化させた鋼を、溶製し、連続鋳
造後（鋳片サイズ：200mm 厚×1240mm幅）、鋳片を手入
れすることなく熱間圧延した。熱間圧延は、スラブ加熱
条件：1090〜1130℃−40〜60分、粗圧延７パス、粗圧延
仕上げ温度：950 〜1000℃、粗圧延仕上げ厚：28mm、仕
上げ（７スタンド）圧延機出側温度：800 〜880 ℃、仕
上げ厚：３mm、コイル巻き取り温度：590 〜700℃、の
条件で行った。得られた熱延コイルを、 880〜920 ℃で
連続焼鈍し、酸洗後、冷間圧延により板厚：0.8 mmに仕
上げたのち、 880〜910 ℃で連続焼鈍後、酸洗して、冷
延焼鈍板とした。 Experiment 2 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.003 to 0.011 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, N
b + V: 0.046 to 0.093 wt% and V / Nb = 2.1 to 4.6,
Ca content: 0.0007wt in the component range of 0.00090.0024wt%
% Was changed to 0.023 wt%, and the steel was melted and continuously cast (slab size: 200 mm thickness x 1240 mm width), and then hot rolled without care of the slab. For hot rolling, slab heating conditions: 1090-1130 ° C-40-60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 950-1000 ° C, rough rolling finished thickness: 28mm, finishing (7 stand) rolling mill exit side The temperature was 800 to 880 ° C, the finished thickness was 3 mm, and the coil winding temperature was 590 to 700 ° C. The obtained hot-rolled coil is continuously annealed at 880 to 920 ° C., pickled, cold rolled to a thickness of 0.8 mm, then continuously annealed at 880 to 910 ° C., pickled and cooled. It was a spread annealing plate.
【００１４】かくして得られた冷延焼鈍板の全長にわた
って表面観察を行い、ヘゲ状欠陥の単位面積当たりの平
均個数を求めた。また、得られた冷延焼鈍板に存在する
酸化物系介在物の定量をブローム法によって行った。得
られた結果を、介在物中の Al2O3量で整理して図２に示
す。得られた結果を、介在物中の Al2O3量で整理して図
２に示す。同図に示したとおり、酸化物系介在物中の A
l2O3量が50wt％を超えるとヘゲ状欠陥が急激に発生し始
めることが判る。これに対し、 Al2O3量が50wt％以下で
はヘゲ状欠陥の発生は少なく、特に Al2O3量が20wt％以
下の場合には、ヘゲ状欠陥の発生はほとんど認められな
かった。なお、観察されたヘゲ状欠陥は、幅が 0.2〜２
mm程度で長さは80〜1000mm程度であった。The surface of the thus obtained cold-rolled annealed sheet was observed over its entire length, and the average number of barbed defects per unit area was determined. In addition, the quantification of oxide-based inclusions present in the obtained cold-rolled annealed sheet was performed by the Brome method. The obtained results are shown in FIG. 2 arranged by the amount of Al 2 O 3 in the inclusions. The obtained results are shown in FIG. 2 arranged by the amount of Al 2 O 3 in the inclusions. As shown in the figure, A in oxide-based inclusions
It can be seen that when the l 2 O 3 content exceeds 50 wt%, barge-like defects begin to rapidly occur. On the other hand, when the Al 2 O 3 content is 50 wt% or less, the occurrence of barbed defects is small, and particularly when the Al 2 O 3 content is 20 wt% or less, almost no barbed defects are observed. . The width of the observed barbed defects was 0.2 to 2 mm.
The length was about 80 mm to 1000 mm.
【００１５】実験３ Ｃ：0.006 〜0.011 wt％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.003 〜0.011 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、N
b＋Ｖ：0.046〜0.093 wt％でかつＶ／Nb＝2.1 〜4.6 、
Al：0.0007〜0.0039wt％の成分範囲で、Ca量を0.0008〜
0.0029wt％の範囲で変化させた鋼を 160トン溶製し、連
続鋳造後（鋳片サイズ：200mm 厚×1240mm幅）、鋳片を
手入れすることなく熱間圧延した。熱間圧延は、スラブ
加熱条件：1090〜1130℃−40〜60分、粗圧延７パス、粗
圧延仕上げ温度：950 〜1000℃、粗圧延仕上げ厚：28m
m、仕上げ（７スタンド）圧延機出側温度：800 〜880
℃、仕上げ厚：３mm、コイル巻き取り温度：590 〜700
℃、の条件で行った。得られた熱延コイルを、 880〜92
0 ℃で連続焼鈍し、酸洗後、冷間圧延により板厚：0.8
mmに仕上げたのち、 880〜910 ℃で連続焼鈍後、酸洗し
て、冷延焼鈍板とした。 Experiment 3 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.003 to 0.011 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, N
b + V: 0.046 to 0.093 wt% and V / Nb = 2.1 to 4.6,
Al: 0.0007-0.0039wt% component range, Ca content 0.0008-
160 tons of steel changed in the range of 0.0029 wt% was melted and continuously cast (slab size: 200 mm thickness x 1240 mm width), and then hot rolled without care. For hot rolling, slab heating conditions: 1090 to 1130 ° C-40 to 60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 950 to 1000 ° C, rough rolling finished thickness: 28m
m, finishing (7 stands) rolling mill outlet temperature: 800 to 880
℃, finishing thickness: 3mm, coil winding temperature: 590-700
° C. The obtained hot-rolled coil is 880-92
Annealed continuously at 0 ° C, pickled, and cold rolled to a thickness of 0.8
After finishing to a mm, the steel sheet was continuously annealed at 880 to 910 ° C. and then pickled to obtain a cold-rolled annealed sheet.
【００１６】かくして得られた冷延焼鈍板の試験片表面
をエメリー＃600 研磨し、塩水噴霧試験（JIS-Z-2371準
拠）を４時間行い、錆の個数をカウントした。また、連
続鋳造後の浸漬ノズルを回収し、ノズル閉塞率を測定し
た。さらに、冷延焼鈍板に存在する酸化物系介在物の定
量をブローム法により行った。得られた結果を、酸化物
系介在物中のTi酸化物量で整理して図３に示す。同図か
ら明らかなように、介在物中のTi酸化物量が20〜90wt％
の範囲にあれば、連鋳時のノズル閉塞がなく、また耐食
性も良好であることが判る。The surface of the test piece of the cold-rolled annealed plate thus obtained was polished with Emery # 600 and subjected to a salt spray test (based on JIS-Z-2371) for 4 hours, and the number of rusts was counted. Further, the immersion nozzle after the continuous casting was recovered, and the nozzle closing rate was measured. Furthermore, the quantification of oxide-based inclusions present in the cold-rolled annealed sheet was performed by the Brome method. The obtained results are shown in FIG. 3 organized by the amount of Ti oxide in the oxide-based inclusions. As is clear from the figure, the content of Ti oxide in the inclusions was 20 to 90 wt%.
It can be seen that when the ratio is within the range, there is no nozzle clogging during continuous casting and the corrosion resistance is good.
【００１７】実験４ Ｃ：0.006 〜0.011 wt％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.003 〜0.011 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、N
b＋Ｖ：0.046〜0.093 wt％でかつＶ／Nb＝2.1 〜4.6 、
Al：0.0007〜0.0026wt％の成分範囲で、Ca量を0.0003〜
0.0055wt％の範囲で変化させた鋼を160 トン溶製し、連
続鋳造後（鋳片サイズ：200mm 厚×1240mm幅）、鋳片を
手入れすることなく熱間圧延した。熱間圧延は、スラブ
加熱条件：1090〜1130℃−40〜60分、粗圧延７パス、粗
圧延仕上げ温度：950 〜1000℃、粗圧延仕上げ厚：28m
m、仕上げ（７スタンド）圧延機出側温度：800 〜880
℃、仕上げ厚：３mm、コイル巻き取り温度：590 〜700
℃、の条件で行った。得られた熱延コイルを、 880〜92
0 ℃で連続焼鈍し、酸洗後、冷間圧延により板厚：0.8
mmに仕上げたのち、 880〜910 ℃で連続焼鈍後、酸洗し
て、冷延焼鈍板とした。 Experiment 4 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.003 to 0.011 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, N
b + V: 0.046 to 0.093 wt% and V / Nb = 2.1 to 4.6,
Al: In the component range of 0.0007-0.0026wt%, the amount of Ca is 0.0003-
160 tons of steel changed in the range of 0.0055 wt% was melted and continuously cast (slab size: 200 mm thickness x 1240 mm width), and then hot rolled without care. For hot rolling, slab heating conditions: 1090 to 1130 ° C-40 to 60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 950 to 1000 ° C, rough rolling finished thickness: 28m
m, finishing (7 stands) rolling mill outlet temperature: 800 to 880
℃, finishing thickness: 3mm, coil winding temperature: 590-700
° C. The obtained hot-rolled coil is 880-92
Annealed continuously at 0 ° C, pickled, and cold rolled to a thickness of 0.8
After finishing to a mm, the steel sheet was continuously annealed at 880 to 910 ° C. and then pickled to obtain a cold-rolled annealed sheet.
【００１８】かくして得られた冷延焼鈍板の試験片表面
をエメリー＃600 研磨し、塩水噴霧試験（JIS-Z-2371準
拠）を４時間行い、錆の個数をカウントした。また、連
続鋳造後の浸漬ノズルを回収し、ノズル閉塞率を測定し
た。さらに、冷延焼鈍板に存在する酸化物系介在物の定
量をブローム法により行った。得られた結果を、酸化物
系介在物中のCaＯ量で整理して図４に示す。同図から明
らかなように、介在物中のCaＯ量が５〜50wt％の範囲に
あれば、連鋳時のノズル閉塞がなく、また耐食性も良好
であることが判る。The test piece surface of the cold-rolled annealed plate thus obtained was polished with Emery # 600, and a salt spray test (based on JIS-Z-2371) was performed for 4 hours, and the number of rusts was counted. Further, the immersion nozzle after the continuous casting was recovered, and the nozzle closing rate was measured. Furthermore, the quantification of oxide-based inclusions present in the cold-rolled annealed sheet was performed by the Brome method. The obtained results are shown in FIG. 4 organized by the amount of CaO in the oxide inclusions. As is clear from the figure, when the CaO content in the inclusions is in the range of 5 to 50 wt%, there is no nozzle blockage during continuous casting and good corrosion resistance.
【００１９】実験５ Ｃ：0.006 〜0.011wt ％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.001 〜0.021 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、N
b＋Ｖ：0.046〜0.093wt ％でかつＶ／Nb：2.1 〜4.6 の
組成範囲で、しかも酸化物系介在物中の Al2O3量が５〜
20wt％と55〜65wt％の２水準について、Ca量を0.0003〜
0.0058wt％の範囲で変化させた鋼を溶製し、連続鋳造後
（鋳片サイズ：200mm 厚×1240mm幅）、鋳片を手入れす
ることなく熱間圧延した。熱間圧延は、スラブ加熱条
件：1090〜1130℃−40〜60分、粗圧延７パス、粗圧延仕
上げ温度：950 〜1000℃、粗圧延仕上げ厚：28mm、仕上
げ（７スタンド）圧延機出側温度：800 〜880 ℃、仕上
げ厚：３mm、コイル巻き取り温度：590 〜700 ℃、の条
件で行った。得られた熱延コイルを、 880〜920 ℃で連
続焼鈍し、酸洗後、冷間圧延により板厚：0.8 mmに仕上
げたのち、 880〜910 ℃で連続焼鈍後、酸洗して、冷延
焼鈍板とした。 Experiment 5 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.001 to 0.021 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, N
b + V: 0.046 to 0.093 wt%, V / Nb: 2.1 to 4.6, and the amount of Al 2 O 3 in the oxide inclusion is 5 to 5.
For two levels of 20wt% and 55 ~ 65wt%, the amount of Ca is 0.0003 ~
The steel was changed in the range of 0.0058 wt%, and after continuous casting (slab size: 200 mm thickness x 1240 mm width), the slab was hot rolled without care. For hot rolling, slab heating conditions: 1090-1130 ° C-40-60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 950-1000 ° C, rough rolling finished thickness: 28mm, finishing (7 stand) rolling mill exit side The temperature was 800 to 880 ° C., the finished thickness was 3 mm, and the coil winding temperature was 590 to 700 ° C. The obtained hot-rolled coil is continuously annealed at 880 to 920 ° C., pickled, cold rolled to a thickness of 0.8 mm, then continuously annealed at 880 to 910 ° C., pickled and cooled. It was a spread annealing plate.
【００２０】かくして得られた冷延焼鈍板の試験片表面
をエメリー＃600 研磨し、塩水噴霧試験（JIS-Z-2371準
拠）を４時間行い、錆の個数をカウントした。ここで、
発錆個数が dm2当たり５個以下の場合をOK、20個以上の
場合をNGとした。図５に、それぞれの Al2O3水準に関し
て行った耐食性評価結果を、Ｓ量とCa量で整理して示
す。同図に示したとおり、酸化物系介在物中の Al2O3量
が50wt％以下の水準では、耐食性が良好なＳ、Ca範囲は
広範囲であるのに対し、 Al2O3量が55〜65wt％の水準で
はその範囲は非常に狭く、耐食性の面から低Ｓ化が必要
不可欠であることが判る。The surface of the test piece of the cold-rolled annealed plate thus obtained was polished with Emery # 600, and a salt spray test (based on JIS-Z-2371) was performed for 4 hours, and the number of rusts was counted. here,
The case where the number of rusting was 5 or less per dm 2 was OK, and the case where the number was 20 or more was NG. FIG. 5 shows the results of the corrosion resistance evaluation performed for each of the Al 2 O 3 levels, organized in terms of the amounts of S and Ca. As shown in the figure, when the amount of Al 2 O 3 in the oxide-based inclusions is 50 wt% or less, the S and Ca range with good corrosion resistance is wide, while the amount of Al 2 O 3 is 55%. At a level of about 65 wt%, the range is very narrow, and it is understood that low S is indispensable from the viewpoint of corrosion resistance.
【００２１】実験６ Ｃ：0.006 〜0.011wt ％、Si：0.22〜0.41wt％、Mn：0.
27〜0.48wt％、Cr：10.9〜11.3wt％、Ｐ：0.021 〜0.04
1 wt％、Ｓ：0.001 〜0.021 wt％、Ｎ：0.004〜0.009 w
t％、Ｏ：0.0037〜0.0076wt％、Ti：0.19〜0.26wt％、A
l：0.0008〜0.0028wt％、Ca：0.0010〜0.0028wt％の組
成範囲で、しかも酸化物系介在物中のTi酸化物量：35〜
80wt％、 Al2O3量：５〜10wt％、CaＯ量：10〜25wt％に
制御しつつ、NbおよびＶ添加量を種々変化させた鋼を溶
製し、連続鋳造後（鋳片サイズ：200mm 厚×1240mm
幅）、鋳片を手入れすることなく熱間圧延した。熱間圧
延は、スラブ加熱条件：1090〜1130℃−40〜60分、粗圧
延７パス、粗圧延仕上げ温度：950 〜1000℃、粗圧延仕
上げ厚：28mm、仕上げ（７スタンド）圧延機出側温度：
800 〜880 ℃、仕上げ厚：３mm、コイル巻き取り温度：
590 〜700 ℃、の条件で行った。得られた熱延コイル
を、 880〜920 ℃で連続焼鈍し、酸洗後、冷間圧延によ
り板厚：0.8 mmに仕上げたのち、 880〜910 ℃で連続焼
鈍後、酸洗して、２Ｄ仕上げの冷延焼鈍板とした。 Experiment 6 C: 0.006 to 0.011 wt%, Si: 0.22 to 0.41 wt%, Mn: 0.
27-0.48 wt%, Cr: 10.9-11.3 wt%, P: 0.021-0.04
1 wt%, S: 0.001 to 0.021 wt%, N: 0.004 to 0.009 w
t%, O: 0.0037-0.0076wt%, Ti: 0.19-0.26wt%, A
l: 0.0008 to 0.0028 wt%, Ca: 0.0010 to 0.0028 wt%, and the amount of Ti oxide in oxide inclusions: 35 to
80wt%, Al 2 O 3 content: 5 to 10 wt%, CaO content: while controlling the 10 to 25 wt%, and smelted steel was varied Nb and V addition amount, after continuous casting (slab Size: 200mm thickness x 1240mm
Width), and the slab was hot-rolled without care. For hot rolling, slab heating conditions: 1090-1130 ° C-40-60 minutes, rough rolling 7 passes, rough rolling finishing temperature: 950-1000 ° C, rough rolling finished thickness: 28mm, finishing (7 stand) rolling mill exit side temperature:
800-880 ° C, Finish thickness: 3mm, Coil winding temperature:
The test was performed at 590 to 700 ° C. The obtained hot-rolled coil is continuously annealed at 880 to 920 ° C., pickled, finished to a sheet thickness of 0.8 mm by cold rolling, continuously annealed at 880 to 910 ° C., and then pickled to obtain 2D. A finished cold rolled annealed plate was used.
【００２２】かくして得られた冷延焼鈍板からＬ方向に
平行にJIS-５号引張試験片を採取し、表面をエメリー＃
600 研磨後、25％の引張りを付加した時の表面粗度（Rm
ax）を測定して、耐リジング性を評価した。なお、判断
基準については、Rmaxが４μm 以下では、リジングが非
常に軽微であると判断し、良好（○）とした。また、４
μm 超え、７μm までは若干リジング発生が確認できる
ためやや不十分（△）とした。さらに、７μm を超える
とリジングが顕著に認識できるため不良（×）とした。
得られた結果をNb，Ｖ量で整理して図６に示す。同図に
示したとおり、Nb、Ｖ量の和が0.04〜0.1 wt％でかつＶ
／Nbが２〜５の範囲では、リジングがほとんど発生しな
いことが判る。A JIS-5 tensile test piece was sampled in parallel with the L direction from the cold-rolled annealed sheet thus obtained, and the surface was emery #
600 After polishing, the surface roughness (Rm
ax) was measured to evaluate ridging resistance. With respect to the criterion, when Rmax was 4 μm or less, the ridging was judged to be very slight, and was judged as good (良好). Also, 4
It is slightly insufficient (△) because the occurrence of ridging can be confirmed slightly above μm and up to 7 μm. Further, when the thickness exceeds 7 μm, the ridging can be remarkably recognized, so that it was judged as defective (×).
FIG. 6 shows the obtained results organized by Nb and V amounts. As shown in the figure, the sum of the amounts of Nb and V is 0.04 to 0.1 wt% and V
It can be seen that when / Nb is in the range of 2 to 5, ridging hardly occurs.
【００２３】以上、述べたとおり、この発明で所期した
目的を達成するためには、鋼中Al量を0.005 wt％以下に
抑制し、かつＶおよびNbを合計量：0.04〜0.1 wt％、Ｖ
／Nb＝2.0 〜5.0 を満足する範囲で添加すると共に、酸
化物系介在物の組成を Al2O3：50wt％以下、Ti酸化物：
20〜90wt％およびCaＯ：５〜50wt％の範囲に制限するこ
とが重要である。しかしながら、酸化物系介在物の組成
を上記の範囲に制御するのは容易ではなく、介在物組成
が上記の範囲になるように鋼組成を成分調整したつもり
でも、介在物組成がばらつきが大きく、必ずしも所望の
組成範囲におさまるわけではないことが判明した。As described above, in order to achieve the desired object of the present invention, in order to suppress the Al content in steel to 0.005 wt% or less, and the total amount of V and Nb: 0.04 to 0.1 wt%, V
/Nb=2.0-5.0 and the composition of the oxide-based inclusions is Al 2 O 3 : 50 wt% or less, Ti oxide:
It is important to limit the range to 20-90 wt% and CaO: 5-50 wt%. However, it is not easy to control the composition of the oxide-based inclusions in the above range, and even if the steel composition is intended to be adjusted so that the inclusion composition is in the above range, the inclusion composition has a large variation, It has been found that the composition does not always fall within the desired composition range.
【００２４】そこで、発明者らは、この点について、さ
らに研究を重ねた結果、酸化物系介在物の組成を上記の
範囲に安定して制御するためには、脱酸剤成分であるA
l、TiおよびCaの添加量もさることながら、これらの成
分を添加する順序が極めて重要であることが判明した。
すなわち、まず、少量のAl添加またはSi添加によって予
備的脱酸を行った後、比較的多量のTiを添加してTi脱酸
を行うと、Al脱酸により生成した Al2O3またはSi脱酸に
より生成したSiO2をTi酸化物が包むような形態のTi酸化
物となり、このような形態のTi酸化物とした上で適量の
Caを添加してやると、所望組成の酸化物系介在物が安定
して得られることが究明されたのである。ここに、上記
のようにして得られた酸化物系介在物は、低融点である
ので連続鋳造時にノズル詰まりを生じることがなく、ま
た、その大きさは５〜20μm 程度にすぎないので製品板
においてクラスター状介在物に起因した表面欠陥が発生
することもない。しかも、この酸化物系介在物の周りに
はCaＳが生成することがないので発錆のおそれもない。Therefore, the inventors have conducted further studies on this point, and as a result, in order to stably control the composition of the oxide-based inclusions within the above range, the deoxidizing agent component A
It turned out that the order in which these components were added was extremely important, as well as the amounts of l, Ti and Ca added.
That is, first, a preliminary deoxidation is performed by adding a small amount of Al or Si, and then a relatively large amount of Ti is added to perform Ti deoxidation, whereby Al 2 O 3 or Si generated by Al deoxidation is removed. It becomes a Ti oxide in a form that the Ti oxide wraps the SiO 2 generated by the acid.
It has been found that when Ca is added, oxide-based inclusions having a desired composition can be stably obtained. Here, the oxide-based inclusions obtained as described above have a low melting point so that nozzle clogging does not occur during continuous casting, and the size is only about 5 to 20 μm. No surface defects due to the cluster-like inclusions are generated. Moreover, since CaS is not generated around the oxide-based inclusions, there is no possibility of rusting.
【００２５】この点、鋼の溶製に際し、脱酸剤成分の添
加順序を特に考慮せずに、合金成分を同時に添加した場
合、特に従来のようにAlを比較的多量に添加した場合に
は、Al2O3 が主体の酸化物が生成し易いため、この発明
で所期したような組成の介在物とはならず、その結果、
所望の効果が得られなかったものと考えられる。また、
この発明では、鋼の溶製段階で、ＶＯＤ炉等を用いた強
攪拌を利用するのに対し、従来は、かような溶製手段を
適切に講じていなかったことも、所望の効果が得られな
かった一因と考えられる。In this regard, when the alloying components are added simultaneously without considering the order of adding the deoxidizing agent components when melting the steel, particularly when a relatively large amount of Al is added as in the prior art, Since an oxide mainly composed of Al 2 O 3 is easily generated, the inclusions do not become inclusions having the composition expected in the present invention.
It is considered that the desired effect was not obtained. Also,
In the present invention, in the step of melting steel, strong stirring using a VOD furnace or the like is used. On the other hand, a desired effect can be obtained because such melting means have not been appropriately taken in the past. It is considered to be one of the reasons for not being able to do so.
【００２６】次に、この発明において、鋼の成分組成を
前記の範囲を限定した理由について説明する。 Ｃ：0.02wt％以下 Ｃは、ｒ値や伸びを低下させる元素である。この発明の
ようにTiの添加を行ってもこれらの特性の面からはＣ量
は低いほど望ましいが、0.02wt％以下であればさほどの
悪影響はないので、Ｃの上限は0.02wt％に定めた。Next, the reason why the composition of the steel is limited to the above range in the present invention will be described. C: 0.02 wt% or less C is an element that lowers the r value and elongation. Even if Ti is added as in the present invention, the lower the C content, the better from the viewpoint of these properties. However, if the content is 0.02 wt% or less, there is no significant adverse effect. Therefore, the upper limit of C is set to 0.02 wt%. Was.
【００２７】Si：1.0 wt％以下 Siは、脱酸のために有効な元素であるが、過剰の添加は
延性の低下を招く。そこで、この発明では 1.0wt％以下
で含有させるものとした。好ましくは 0.7wt％以下であ
る。Si: 1.0 wt% or less Si is an effective element for deoxidation, but excessive addition causes a decrease in ductility. Therefore, in the present invention, the content is set to 1.0 wt% or less. Preferably it is 0.7 wt% or less.
【００２８】Mn：1.0 wt％以下 Mnは、脱酸のために有効な元素であるが、オーステナイ
ト安定化元素であり、過剰の添加は高温でγ相を生成
し、最終冷延焼鈍板において延性の低下を招くので、
1.0wt％以下で含有させるものとした。Mn: 1.0 wt% or less Mn is an element effective for deoxidation, but is an austenite stabilizing element. Excessive addition generates a γ phase at a high temperature and causes ductility in the final cold-rolled annealed sheet. Cause a decrease in
The content was 1.0 wt% or less.
【００２９】Cr：５〜50wt％ Crは、耐食性を確保する上で必要不可欠な元素である
が、含有量が５wt％未満ではその添加効果に乏しく、一
方50wt％を超えると延性や靱性の劣化が著しくなるの
で、５〜50wt％の範囲で含有させるものとした。Cr: 5 to 50 wt% Cr is an indispensable element for ensuring corrosion resistance. However, if the content is less than 5 wt%, the effect of its addition is poor, while if it exceeds 50 wt%, ductility and toughness deteriorate. , The content was set to be in the range of 5 to 50 wt%.
【００３０】Ｐ：0.05wt％以下 Ｐは、延性や靱性に有害な元素であり、含有量が0.05wt
％を超えるとその弊害が顕著となるので、0.05wt％以下
に制限した。P: 0.05 wt% or less P is an element harmful to ductility and toughness, and its content is 0.05 wt.
%, The adverse effect becomes remarkable. Therefore, the content was limited to 0.05 wt% or less.
【００３１】Ｓ：0.015 wt％以下 前述したように、Ｓは耐食性を低下させる元素である。
とりわけ、この発明のようにCa添加を行う場合には水溶
性であるCaＳを生じ易い。添加するCa量にも依存する
が、この発明の主眼である酸化物系介在物組成をコント
ロールしても、Ｓ量が 0.015wt％を超えると耐食性の劣
化が生じ易くなるので、Ｓ量は 0.015wt％以下に制限し
た。S: 0.015 wt% or less As described above, S is an element that lowers corrosion resistance.
In particular, when Ca is added as in the present invention, water-soluble CaS is easily generated. Although depending on the amount of Ca added, even if the composition of the oxide-based inclusions, which is the main feature of the present invention, is controlled, if the amount of S exceeds 0.015 wt%, deterioration of corrosion resistance is likely to occur. It was limited to wt% or less.
【００３２】Ｎ：0.02wt％以下 Ｎも、Ｃと同様にｒ値と伸びに有害な元素であり、低け
れば低いほど好ましいが、0.02wt％を超えなければさほ
どの悪影響はないので、上限を0.02wt％に定めた。N: 0.02 wt% or less N is also an element harmful to the r value and elongation like C, and the lower, the better, but the more it does not exceed 0.02 wt%, there is no significant adverse effect. It was set to 0.02 wt%.
【００３３】Al：0.005 wt％以下 実験１の結果からも明らかなように、冷延板表面品質の
点から 0.005wt％以下にする必要がある。すなわち、含
有量が 0.005wt％を超えると表面に Al2O3の凝集に起因
した巨大なヘゲ状欠陥が生じるからである。Al: 0.005 wt% or less As is clear from the results of Experiment 1, it is necessary to make the content 0.005 wt% or less from the viewpoint of the cold rolled sheet surface quality. That is, if the content exceeds 0.005 wt%, huge barbed defects due to aggregation of Al 2 O 3 occur on the surface.
【００３４】Ｏ：0.01wt％以下 酸素は鋼中には全く固溶せず、酸化物として存在する。
介在物は錆や破壊の起点となり易く、特に酸素量が0.01
wt％を超えるとその悪影響が顕著となるので、Ｏ量は0.
01wt％以下に制限した。O: 0.01 wt% or less Oxygen does not form a solid solution in steel at all and exists as an oxide.
Inclusions tend to be the starting point of rust and destruction, especially when the oxygen content is 0.01
If the content exceeds wt%, the adverse effect becomes remarkable.
It was limited to 01 wt% or less.
【００３５】Ti：0.08wt％以上かつ６×（Ｃ＋Ｎ）以
上、0.5 wt％以下 Tiは、成形加工性の向上に必要不可欠な元素であるだけ
でなく、脱酸にも有効な元素である。前者の成形加工性
向上の点からは、６×（Ｃ＋Ｎ）以上が必要であり、ま
た、脱酸を有効に行ってなおかつＣ，Ｎに対しても有効
に作用するためには0.08wt％が必要である。従って、Ti
の下限は0.08wt％でかつ６×（Ｃ＋Ｎ）に限定される。
一方、Ti量が 0.5wt％を超えると延性が低下しはじめる
ので、Ti量の上限は 0.5wt％に定めた。Ti: 0.08% by weight or more and 6 × (C + N) or more and 0.5% by weight or less Ti is an element not only indispensable for improving the formability but also effective for deoxidation. In view of the former improvement in moldability, 6 × (C + N) or more is required, and 0.08 wt% is required for effective deoxidation and effective action on C and N. is necessary. Therefore, Ti
Is 0.08 wt% and is limited to 6 × (C + N).
On the other hand, if the Ti content exceeds 0.5 wt%, the ductility starts to decrease, so the upper limit of the Ti content is set to 0.5 wt%.
【００３６】Nb＋Ｖ：0.04〜0.1 wt％でかつＶ／Nb＝2.
0 〜5.0 Nb, Ｖはいずれも、耐リジング性の改善に極めて有効な
元素である。実験６で示したように、耐リジング性の改
善効果は、NbおよびＶの合計量が0.04〜0.1 wt％でかつ
これらの比Ｖ／Nbが 2.0〜5.0 の範囲で顕著なために、
この範囲に限定した。耐リジング性の改善にNb, Ｖが有
効に作用する理由は、現在までのところまだ明確に解明
されたわけではないが、熱延時における（００１）バン
ド状組織の破壊にNb，Ｖ炭窒化物の析出が有効に作用し
たものと考えられる。Nb + V: 0.04 to 0.1 wt% and V / Nb = 2.
Each of 0 to 5.0 Nb and V is an extremely effective element for improving ridging resistance. As shown in Experiment 6, the effect of improving ridging resistance was remarkable because the total amount of Nb and V was 0.04 to 0.1 wt% and the ratio V / Nb was 2.0 to 5.0.
Limited to this range. The reason why Nb, V effectively acts to improve the ridging resistance has not been clearly elucidated so far, but Nb, V carbonitride has an effect on the breaking of the (001) band-like structure during hot rolling. It is considered that the precipitation worked effectively.
【００３７】Ca：0.0005wt％以上、0.0050wt％以下 Caは、この発明に係る酸化物系介在物の融点を効果的に
低下して、連続鋳造時におけるノズル閉塞を防止するの
に極めて有効な元素であり、その効果は0.0005wt％以上
で顕著であるので、下限は0.0005wt％とした。一方、多
量に添加すると耐食性の劣化を招き、そのおそれが0.00
50wt％を超えると顕著になるので、上限は0.0050wt％と
した。Ca: not less than 0.0005 wt% and not more than 0.0050 wt% Ca is extremely effective in effectively lowering the melting point of the oxide-based inclusion according to the present invention and preventing nozzle clogging during continuous casting. Since the element is an element and its effect is remarkable at 0.0005 wt% or more, the lower limit is set to 0.0005 wt%. On the other hand, if added in large amounts, corrosion resistance is degraded, and the
Since it becomes remarkable when it exceeds 50 wt%, the upper limit is made 0.0050 wt%.
【００３８】以上、基本成分について説明したが、この
発明では、必要応じて次の元素をそれぞれ適宜添加する
ことができる。 Mo：0.05〜4.0 wt％ Moは、耐食性向上に非常に有効な元素であり、その効果
は0.05wt％以上で顕著になるので、下限は0.05wt％とし
た。一方、Moは添加すればするほど耐食性は向上する
が、4.0 wt％を超えるとほぼその効果は飽和に達するば
かりでなく、靱性や延性の著しい低下を招くので、上限
は 4.0wt％とした。Although the basic components have been described above, in the present invention, the following elements can be appropriately added as needed. Mo: 0.05 to 4.0 wt% Mo is a very effective element for improving corrosion resistance, and its effect becomes remarkable at 0.05 wt% or more. Therefore, the lower limit is set to 0.05 wt%. On the other hand, the more Mo is added, the more the corrosion resistance is improved. However, if Mo exceeds 4.0 wt%, not only the effect almost reaches saturation, but also a remarkable decrease in toughness and ductility is caused, so the upper limit was made 4.0 wt%.
【００３９】Ｂ：0.0002〜0.0030wt％ Ｂは、深絞り後にさらに加工される場合に問題となる２
次加工脆性を防止するのに有用な元素であるが、含有量
が0.0002wt％に満たないとその添加効果に乏しく、一方
0.0030wt％を超えると延性が低下しはじめるので、Ｂは
0.0002〜0.0030wt％の範囲で含有させるものとした。B: 0.0002 to 0.0030 wt% B is a problem when further processing is performed after deep drawing 2
It is a useful element to prevent secondary working embrittlement, but if its content is less than 0.0002wt%, the effect of its addition is poor.
If the content exceeds 0.0030 wt%, the ductility starts to decrease.
It was contained in the range of 0.0002 to 0.0030 wt%.
【００４０】次に、この発明において、酸化物系介在物
組成を前記の範囲を限定した理由について説明する。 Ti酸化物量：20〜90wt％、 Al2O3：50wt％以下、CaＯ：
５〜50wt％ 酸化物系介在物の組成を上記の範囲にしたところが、こ
の発明の主眼技術である。先に実験２，３，４，５で示
したように、 Al2O3量を50wt％以下、より好ましくは20
wt％以下とすることによって、冷延板で生成するヘゲ状
表面欠陥を防止でき、さらにTi酸化物量を20〜90wt％、
CaＯ量を５〜50wt％とすることによって、連続鋳造時に
おけるノズル詰まりを防止でき、しかも耐食性の劣化も
ない。従って、この発明では、脱酸生成物に起因した酸
化物系介在物の組成について、Ti酸化物：20〜90wt％、
Al2O3：50wt％以下、CaＯ：５〜50wt％の範囲に限定し
たのである。さらに、酸化物系介在物の組成をこの範囲
に制限すると、冷延焼鈍板の深絞り加工性の指標である
ｒ値が向上し、同時に面内異方性Δｒも小さくなること
が見出された。この理由については、まだ明確に解明さ
れたわけではないが、再結晶時の集合組織形成に介在物
形態が影響を及ぼしたものと推察される。Next, the reason for limiting the range of the oxide-based inclusion composition in the present invention will be described. Ti oxide content: 20~90wt%, Al 2 O 3 : 50wt% or less, CaO:
The main technology of the present invention is that the composition of the oxide-based inclusions is within the above range. As previously shown in Experiments 2, 3, 4, and 5, the amount of Al 2 O 3 was reduced to 50 wt% or less, more preferably 20 wt% or less.
By setting the content to not more than wt%, barbed surface defects generated in the cold rolled sheet can be prevented.
By setting the CaO content to 5 to 50 wt%, nozzle clogging during continuous casting can be prevented, and there is no deterioration in corrosion resistance. Therefore, in the present invention, regarding the composition of the oxide-based inclusions caused by the deoxidation product, Ti oxide: 20 to 90 wt%,
Al 2 O 3 : limited to 50 wt% or less, CaO: limited to 5 to 50 wt%. Further, when the composition of the oxide-based inclusions is limited to this range, it has been found that the r value, which is an index of the deep drawability of the cold-rolled annealed sheet, is improved, and the in-plane anisotropy Δr is also reduced. Was. The reason for this has not been clarified yet, but it is presumed that the inclusion morphology affected the texture formation during recrystallization.
【００４１】なお、この発明では、鋼中の全ての介在物
を、上記の組成の複合酸化物とする必要はなく、少なく
とも50％、好ましくは70％以上がかような Al2O3−Ti酸
化物−CaＯ系複合酸化物になっていれば良い。ここに、
その他に生成される酸化物としては、SiO2, MnO, FeOX
およびMgO などが考えられる。In the present invention, it is not necessary for all inclusions in the steel to be a composite oxide having the above composition, and at least 50%, preferably 70% or more of Al 2 O 3 —Ti What is necessary is just to be an oxide-CaO-based composite oxide. here,
Other oxides generated include SiO 2 , MnO, FeO X
And MgO.
【００４２】次に、この発明の好適製造方法について説
明する。この発明では、前述したとおり、溶製段階にお
ける脱酸剤成分の添加順序が重要である。すなわち、ま
ず、少量のAlまたはSiを添加して予備的脱酸を行ったの
ち、比較的多量のTiを添加してTi脱酸を行う。このよう
にすると、AlまたはSi脱酸により生成した Al2O3やSiO2
がTi酸化物で包まれたような形態のTi酸化物となるが、
かような形態のTi酸化物の大きさは５〜20μm 程度であ
るので、製品板において巨大のクラスター状介在物に起
因した表面欠陥を有利に防止することができる。しかし
ながら、かかるTi酸化物は、溶鋼中では固相であるた
め、このままでは連続鋳造時に地鉄を取り込んだ形でタ
ンディッシュのノズル内面に付着・堆積して、ノズルの
閉塞を生じるおそれがある。しかしながら、その後にCa
を適量添加してやると、低融点の酸化物となり、それ故
連続鋳造時におけるノズル詰まりが有利に回避されるの
である。しかも、かかる酸化物系介在物の周りにはCaＳ
が生成することがないので発錆も併せて防止できること
は前述したとおりである。Next, a preferred production method of the present invention will be described. In the present invention, as described above, the order of addition of the deoxidizer component in the melting step is important. That is, first, a small amount of Al or Si is added to perform preliminary deoxidation, and then a relatively large amount of Ti is added to perform Ti deoxidation. In this way, Al 2 O 3 or SiO 2 generated by deoxidation of Al or Si
Is a form of Ti oxide wrapped in Ti oxide,
Since the size of the Ti oxide in such a form is about 5 to 20 μm, it is possible to advantageously prevent surface defects due to huge cluster-like inclusions on the product plate. However, since the Ti oxide is a solid phase in the molten steel, there is a possibility that the titanium oxide may adhere and accumulate on the inner surface of the nozzle of the tundish in a form in which the ground iron is taken in during continuous casting, and the nozzle may be clogged. However, then Ca
When an appropriate amount is added, a low-melting-point oxide is obtained, so that nozzle clogging during continuous casting is advantageously avoided. In addition, around such oxide-based inclusions, CaS
As described above, since rust is not generated, rusting can also be prevented.
【００４３】上記のようにして、所望の鋼組成および介
在物組成に調整した溶鋼は、常法に従って、鋳造、熱間
圧延、冷間圧延および焼鈍処理を施して製品とされる。
ここに、好適な熱延条件、冷延条件および焼鈍条件は次
のとおりである。熱延条件 スラブ加熱温度：1050〜1260℃、粗圧延温度：900 〜11
80℃、粗圧延トータル圧下率：80〜93％、仕上げ圧延温
度：750 〜1000℃、仕上げ圧延出側厚さ：1.5〜７mm、
巻取り温度：400 〜850 ℃。冷延条件 冷間圧延は、タンデムミル、クラスターミルまたはゼン
ジミィアーミルにより圧延できる。総圧下率は45〜95％
程度が好ましい。冷間圧延−焼鈍−冷間圧延を繰り返し
ても良い。焼鈍条件 仕上げ焼鈍温度：800 〜1100℃の範囲で、目的とする材
質に応じて選択する。目標温度保持時間：０〜1800ｓの
範囲で、目的とする材質に応じて選択する。また、表面
仕上げについては、２Ｄ、２Ｂ、ＢＡおよび研磨などが
ある。The molten steel adjusted to the desired steel composition and inclusion composition as described above is cast, hot-rolled, cold-rolled, and annealed in a conventional manner to obtain a product.
Here, suitable hot rolling conditions, cold rolling conditions and annealing conditions are as follows. Hot rolling conditions Slab heating temperature: 1050-1260 ° C, rough rolling temperature: 900-11
80 ° C, total rolling reduction: 80-93%, finishing rolling temperature: 750-1000 ° C, finish rolling exit side thickness: 1.5-7mm,
Winding temperature: 400-850 ° C. Cold Rolling Conditions Cold rolling can be performed by a tandem mill, a cluster mill or a Sendzimir mill. Total rolling reduction 45-95%
The degree is preferred. Cold rolling-annealing-cold rolling may be repeated. Annealing conditions Finish annealing temperature: Select from 800 to 1100 ° C according to the target material. Target temperature holding time: Select from the range of 0 to 1800 s according to the target material. The surface finish includes 2D, 2B, BA and polishing.
【００４４】[0044]
【実施例】表１に示す成分組成の溶鋼を次のようにして
溶製した。すなわち、脱炭処理後の含クロム溶鋼に対
し、ＶＯＤ炉にて、溶鋼攪拌下に、まず所定量のAlを添
加して予備脱酸を行い、ついでTiを添加してTi脱酸を行
ったのち、成分調整を行い、溶鋼を大気中に移してから
Ca添加を行った。ついで、連続鋳造法にて、厚み：200
mm、幅：1000mmサイズに鋳造した。得られたスラブは手
入れすることなく、次の条件で熱間圧延を行った。 スラブ加熱温度：1100〜1170℃、加熱時間：30〜90分、
粗７パス、粗仕上げ厚み：25mm、粗圧延終了温度：960
〜1060℃、仕上げ（７段ミル）、仕上げ厚：３mm、ＦＤ
Ｔ：800 〜950 ℃、ＣＴ：460 〜680 ℃。EXAMPLES Molten steel having the composition shown in Table 1 was produced as follows. That is, to the chromium-containing molten steel after the decarburization treatment, in a VOD furnace, while stirring the molten steel, a predetermined amount of Al was first added to perform preliminary deoxidation, and then Ti was added to perform Ti deoxidation. After that, adjust the composition and transfer the molten steel to the atmosphere.
Ca addition was performed. Then, by continuous casting method, thickness: 200
mm, width: cast to 1000mm size. The obtained slab was hot-rolled under the following conditions without care. Slab heating temperature: 1100-1170 ° C, heating time: 30-90 minutes,
Rough 7 passes, rough finish thickness: 25mm, rough rolling end temperature: 960
~ 1060 ℃, Finish (7-step mill), Finish thickness: 3mm, FD
T: 800 to 950 ° C, CT: 460 to 680 ° C.
【００４５】得られた熱延コイルを、 900〜1000℃で連
続焼鈍し、酸洗後、冷間圧延により板厚：0.6 mmに仕上
げたのち、 870〜1000℃で連続焼鈍後、酸洗して冷延焼
鈍板とした。かくして得られた冷延焼鈍板について、酸
化物系介在物の組成、連鋳後のノズル閉塞率、板表面の
ヘゲ欠陥個数ならびに冷延焼鈍板のｒ値、Δｒ値、２次
加工脆性割れ発生温度およびリジング高さについて調べ
た結果を、表２に示す。また、同表には、冷延焼鈍板表
面をエメリー＃600 研磨し、塩水噴霧試験（ＳＳＴ）と
塩乾湿複合サイクル腐食試験を行った後の発錆個数と発
錆面積率について調査した結果も併せて示す。成形加工
性については、ｒ値、Δｒ値および２次加工脆性割れ発
生温度で、また表面性状については、冷延板における表
面欠陥発生個数で、さらに耐食性については、塩水噴霧
試験および塩乾湿複合サイクル腐食試験における発錆個
数および発錆面積率で、またさらに耐リジング性につい
ては表面粗さ（Rmax）で、それぞれ評価した。The obtained hot-rolled coil was continuously annealed at 900 to 1000 ° C., pickled, finished to a thickness of 0.6 mm by cold rolling, continuously annealed at 870 to 1000 ° C., and pickled. To form a cold-rolled annealed plate. About the obtained cold rolled annealed sheet, the composition of the oxide-based inclusions, the nozzle clogging rate after continuous casting, the number of barge defects on the sheet surface, the r value of the cold rolled annealed sheet, the Δr value, and the secondary work brittle crack Table 2 shows the results of examining the generation temperature and ridging height. The table also shows the results of investigation on the number of rusts and the area ratio of rust after the surface of the cold-rolled annealed plate was polished with Emery # 600 and subjected to the salt spray test (SST) and the salt-dry / wet combined cycle corrosion test. Also shown. For the formability, the r value, Δr value and the temperature at which secondary working brittle cracks occur, for the surface properties, the number of surface defects generated in cold-rolled sheets, and for the corrosion resistance, for the salt spray test and the salt-dry / wet combined cycle The number of rusts and the area ratio of rust in the corrosion test were evaluated, and the ridging resistance was evaluated by the surface roughness (Rmax).
【００４６】なお、それぞれの特性評価方法は次のとお
りである。 ・冷延焼鈍板中の酸化物系介在物の分析 冷延焼鈍板から試験片を採取し、臭素メタノール系の溶
液中で電解することによって酸化物系介在物を残査とし
て採取したのち、酸に溶解して化学分析を行った。 ・ノズル閉塞率測定法 160 トン連続鋳造後の初期径：60mmのノズルを回収し、
断面を切断して最小径を測定し、（（初期径−鋳込み後
の最小径）／初期径）× 100（％）を閉塞率とした。The respective characteristic evaluation methods are as follows.・ Analysis of oxide-based inclusions in cold-rolled annealed plate A test piece was collected from the cold-rolled annealed plate, and the oxide-based inclusions were collected as a residue by electrolysis in a bromine-methanol-based solution. And subjected to chemical analysis.・ Nozzle clogging rate measurement method The initial diameter after continuous casting of 160 tons: 60 mm nozzle was collected,
The cross section was cut and the minimum diameter was measured, and ((initial diameter−minimum diameter after casting) / initial diameter) × 100 (%) was defined as the closing ratio.
【００４７】・ｒ値、Δｒ値測定 ｒ値は、フェライト系ステンレス鋼の深絞り加工性を示
す指標である。冷延焼鈍板からＬ、 Ｄ、 Ｃ方向に平行に
JIS 13号Ｂ引張試験片を採取し、JIS Z 2241に準拠した
引張試験を行い、相当歪みが15％の場合でランクフォー
ド値（ｒ値）を測定した。この時にＬ、 Ｄ、 Ｃ方向の加
重平均をｒ値とした。また、面内異方性を示すΔｒは、
（Ｌ方向ｒ値＋Ｃ方向ｒ値−２×Ｄ方向ｒ値）／２によ
り算出した。 ・２次加工脆性割れ発生温度 絞り比：２で深絞り加工したカップ状試験片を-100〜20
℃の特定温度に保持したのち、落重試験（おもり重量：
５kg、落差：0.8 ｍ）によりカップ頭部に衝撃荷重を付
加し、カップ側壁部における脆性割れの有無から、割れ
発生温度を求めた。 ・リジング高さ 冷延焼鈍板からＬ方向に平行にJIS-５号引張試験片を採
取し、表面をエメリー#600研磨後、25wt％の引張りを付
加した時の表面粗さ（Rmax）を測定し、リジング高さと
した。Measurement of r value and Δr value The r value is an index indicating the deep drawability of ferritic stainless steel. From the cold-rolled annealed plate parallel to the L, D, C directions
A JIS No. 13B tensile test piece was sampled and subjected to a tensile test in accordance with JIS Z 2241. When the equivalent strain was 15%, the Rankford value (r value) was measured. At this time, the weighted average in the L, D, and C directions was defined as the r value. Δr indicating in-plane anisotropy is
(L value in the L direction + r value in the C direction−2 × r value in the D direction) / 2.・ Secondary processing brittle crack initiation temperature -100 to 20 cup-shaped test pieces deep drawn at a drawing ratio of 2:
After holding at a specific temperature of ° C, drop weight test (weight:
An impact load was applied to the cup head by 5 kg (head: 0.8 m), and the crack initiation temperature was determined from the presence or absence of brittle cracks on the side wall of the cup.・ Ridging height A JIS-5 tensile test piece is sampled from the cold-rolled annealed plate in parallel with the L direction, and after polishing the surface with Emery # 600, the surface roughness (Rmax) is measured when 25 wt% tension is applied. And the ridging height.
【００４８】・塩水噴霧試験（ＳＳＴ） 冷延焼鈍板表面をエメリー＃600 研磨仕上げ後、脱脂
し、JIS Z 2371に準拠した条件で塩水噴霧試験を４ｈ行
い、発錆個数をカウントした。 ・塩乾湿複合サイクル腐食試験（ＣＣＴ） 冷延焼鈍板表面をエメリー＃600 研磨仕上げ後、脱脂
し、35℃で 3.5％NaClを0.5 時間噴霧後、１ｈの乾燥
（60℃）および１ｈ湿潤（40℃、相対湿度：95％以上）
を１サイクルとした複合腐食試験を10サイクル実施し、
発錆面積率を測定した。Salt Spray Test (SST) After the surface of the cold-rolled annealed plate was polished with Emery # 600, degreased and subjected to a salt spray test under the conditions in accordance with JIS Z 2371 for 4 hours, and the number of rusting was counted.・ Salt dry / wet combined cycle corrosion test (CCT) After the surface of the cold rolled annealed plate is polished with Emery # 600, degreased, sprayed with 3.5% NaCl at 35 ° C for 0.5 hour, dried for 1 hour (60 ° C) and wet for 1 hour (40 hours) ° C, relative humidity: 95% or more)
10 cycles of a complex corrosion test with 1 cycle
The rusting area ratio was measured.
【００４９】[0049]
【表１】 [Table 1]
【００５０】[0050]
【表２】 [Table 2]
【００５１】表２に示したとおり、この発明に従うフェ
ライト系ステンレス鋼は、その溶製後の連続鋳造時にお
いてノズル閉塞が全く生じず、また製品板においても、
表面欠陥が全くなく、しかもｒ値が 1.7以上でかつΔｒ
が 0.2以下という優れた成形加工性および表面粗度（Rm
ax）が 2.6μm 以下という優れた耐リジング性を有して
おり、さらに耐食性にも優れていた。As shown in Table 2, the ferritic stainless steel according to the present invention has no nozzle clogging at the time of continuous casting after its smelting.
No surface defects, r value of 1.7 or more and Δr
Formability and surface roughness (Rm
ax) had excellent ridging resistance of 2.6 μm or less, and was also excellent in corrosion resistance.
【００５２】[0052]
【発明の効果】かくして、この発明によれば、優れた成
形加工性を有するのはいうまでもなく、酸化物系介在物
に起因した表面欠陥がなく、また耐食性、さらには耐リ
ジング性にも優れたフェライト系ステンレス鋼を安定し
て得ることができる。また、この発明のフェライト系ス
テンレス鋼は、その製造過程の連続鋳造時においてノズ
ル閉塞が生じることもない。Thus, according to the present invention, it is needless to say that the present invention has excellent moldability, no surface defects due to oxide inclusions, and corrosion resistance and ridging resistance. Excellent ferritic stainless steel can be obtained stably. Further, the ferritic stainless steel of the present invention does not cause nozzle blockage during continuous casting in the production process.
【図１】鋼中のT.Al量と熱延焼鈍板の表面欠陥個数との
関係を示したグラフである。FIG. 1 is a graph showing the relationship between the amount of T.Al in steel and the number of surface defects of a hot-rolled annealed sheet.
【図２】酸化物系介在物中の Al2O3濃度とヘゲ状表面欠
陥個数との関係を示したグラフである。FIG. 2 is a graph showing the relationship between the concentration of Al 2 O 3 in oxide-based inclusions and the number of barbed surface defects.
【図３】酸化物系介在物中のTi酸化物濃度とノズル閉塞
率および発錆個数との関係を示したグラフである。FIG. 3 is a graph showing the relationship between the concentration of Ti oxide in oxide-based inclusions, the nozzle closing rate, and the number of rusting.
【図４】酸化物系介在物中のCaＯ濃度とノズル閉塞率お
よび発錆個数との関係を示したグラフである。FIG. 4 is a graph showing the relationship between the CaO concentration in oxide-based inclusions, the nozzle clogging rate, and the number of rusting.
【図５】耐食性に及ぼすＳ量とCa量の影響を、２つの A
l2O3水準で比較して示したグラフである。FIG. 5 shows the effect of S content and Ca content on corrosion resistance in two A
It is a graph shown by comparison at l 2 O 3 level.
【図６】リジングの発生程度に及ぼすNbおよびＶの影響
を示したグラフである。FIG. 6 is a graph showing the effects of Nb and V on the occurrence of ridging.
フロントページの続き (72)発明者 佐藤 進 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 (72)発明者 岸本 康夫 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 (72)発明者 三木 祐司 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 (72)発明者 反町 健一 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内Continuing from the front page (72) Inventor Susumu Sato 1 Kawasaki-cho, Chuo-ku, Chiba-shi, Chiba Pref. Kawasaki Steel Engineering Co., Ltd. (72) Inventor Yasuo Kishimoto 1-Kawasaki-cho, Chuo-ku, Chiba-shi Chiba Pref. (72) Inventor Yuji Miki 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Kawasaki Steel Corporation (72) Inventor Kenichi Sorimachi 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Kawasaki Steel Co., Ltd. Inside the company technology laboratory
Claims (3)
生成物に起因した酸化物系介在物の組成が、Ti酸化物：
20〜90wt％、 Al2O3：50wt％以下およびCaＯ：５〜50wt
％の範囲を満足することを特徴とする表面性状が良好で
耐食性、成形加工性および耐リジング性に優れたフェラ
イト系ステンレス鋼。[Claim 1] C: 0.02 wt% or less, Si: 1.0 wt% or less, Mn: 1.0 wt% or less, Cr: 5 to 50 wt%, P: 0.05 wt% or less, S: 0.015 wt% or less, N: 0.02 wt% or less, Al: 0.005 wt% or less, O: 0.01 wt% or less, Ti: 0.08 wt% or more and 6 × (C + N) or more, 0.5 wt% or less, (V + Nb): 0.04 to 0.1 wt% and V / Nb = 2.0-5.0, Ca: 0.0005-0.0050wt%, the balance is substantially Fe composition, and the composition of oxide inclusions caused by deoxidation products in steel is Ti oxide :
20~90wt%, Al 2 O 3: 50wt% or less, and CaO: 5-50 wt
% Ferritic stainless steel with good surface properties and excellent corrosion resistance, moldability and ridging resistance.
で耐食性、成形加工性および耐リジング性に優れたフェ
ライト系ステンレス鋼。2. The steel composition according to claim 1, wherein the steel composition further comprises Mo: 0.05 to 4.0 wt%, and has excellent surface properties and excellent corrosion resistance, moldability and ridging resistance. Ferritic stainless steel.
さらに Ｂ：0.0002〜0.0030wt％ を含有する組成になることを特徴とする表面性状が良好
で耐食性、成形加工性および耐リジング性に優れたフェ
ライト系ステンレス鋼板。3. The steel composition according to claim 1, wherein the steel composition is
Further, B: a ferritic stainless steel sheet which has a composition containing 0.0002 to 0.0030 wt% and has excellent surface properties and excellent corrosion resistance, moldability and ridging resistance.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17187998A JP3661419B2 (en) | 1998-06-18 | 1998-06-18 | Ferritic stainless steel with good surface properties and excellent corrosion resistance, molding processability and ridging resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP17187998A JP3661419B2 (en) | 1998-06-18 | 1998-06-18 | Ferritic stainless steel with good surface properties and excellent corrosion resistance, molding processability and ridging resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2000001757A true JP2000001757A (en) | 2000-01-07 |
| JP3661419B2 JP3661419B2 (en) | 2005-06-15 |
Family
ID=15931496
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP17187998A Expired - Fee Related JP3661419B2 (en) | 1998-06-18 | 1998-06-18 | Ferritic stainless steel with good surface properties and excellent corrosion resistance, molding processability and ridging resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3661419B2 (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2818289A1 (en) * | 2000-12-15 | 2002-06-21 | Usinor | Stainless steel for severe working and notably for deep drawing of rolled and heat treated steel sheet with controlled selection of inclusions |
| FR2818290A1 (en) * | 2000-12-15 | 2002-06-21 | Ugine Savoie Imphy | Stainless steel for shaping by severe working and notably by cold striking or drawing into small diameter wires, with a controlled composition for selection of the type and dimensions of its inclusions |
| EP1452616A1 (en) * | 2001-12-06 | 2004-09-01 | Nippon Steel Corporation | Ferritic stainless steel sheet excellent in press formability and workability and method for production thereof |
| JP2012184494A (en) * | 2011-03-08 | 2012-09-27 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic stainless steel excellent in rusting resistance |
-
1998
- 1998-06-18 JP JP17187998A patent/JP3661419B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| FR2818289A1 (en) * | 2000-12-15 | 2002-06-21 | Usinor | Stainless steel for severe working and notably for deep drawing of rolled and heat treated steel sheet with controlled selection of inclusions |
| FR2818290A1 (en) * | 2000-12-15 | 2002-06-21 | Ugine Savoie Imphy | Stainless steel for shaping by severe working and notably by cold striking or drawing into small diameter wires, with a controlled composition for selection of the type and dimensions of its inclusions |
| EP1452616A1 (en) * | 2001-12-06 | 2004-09-01 | Nippon Steel Corporation | Ferritic stainless steel sheet excellent in press formability and workability and method for production thereof |
| EP1452616A4 (en) * | 2001-12-06 | 2006-08-02 | Nippon Steel & Sumikin Sst | Ferritic stainless steel sheet excellent in press formability and workability and method for production thereof |
| US7341637B2 (en) | 2001-12-06 | 2008-03-11 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic stainless steel sheet excellent in press formability and workability and method for production thereof |
| JP2012184494A (en) * | 2011-03-08 | 2012-09-27 | Nippon Steel & Sumikin Stainless Steel Corp | Ferritic stainless steel excellent in rusting resistance |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3661419B2 (en) | 2005-06-15 |
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