JPH0353026A - Manufacture of ferritic stainless steel sheet having excellent heat resistance and corrosion resistance - Google Patents
Manufacture of ferritic stainless steel sheet having excellent heat resistance and corrosion resistanceInfo
- Publication number
- JPH0353026A JPH0353026A JP18601389A JP18601389A JPH0353026A JP H0353026 A JPH0353026 A JP H0353026A JP 18601389 A JP18601389 A JP 18601389A JP 18601389 A JP18601389 A JP 18601389A JP H0353026 A JPH0353026 A JP H0353026A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- ferritic stainless
- hot
- rolling
- cold
- 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.)
- Granted
Links
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 50
- 230000007797 corrosion Effects 0.000 title claims abstract description 28
- 238000005260 corrosion Methods 0.000 title claims abstract description 28
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 25
- 238000001816 cooling Methods 0.000 claims abstract description 38
- 238000005097 cold rolling Methods 0.000 claims abstract description 32
- 230000009467 reduction Effects 0.000 claims abstract description 31
- 238000005098 hot rolling Methods 0.000 claims abstract description 26
- 238000005096 rolling process Methods 0.000 claims abstract description 25
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 14
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 10
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 9
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 8
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 8
- 150000002910 rare earth metals Chemical class 0.000 claims abstract description 6
- 238000000034 method Methods 0.000 claims description 18
- 238000000137 annealing Methods 0.000 claims description 15
- 238000010438 heat treatment Methods 0.000 claims description 14
- 238000004804 winding Methods 0.000 claims description 8
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 229910052735 hafnium Inorganic materials 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 229910052715 tantalum Inorganic materials 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 229910052796 boron Inorganic materials 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 229910000859 α-Fe Inorganic materials 0.000 abstract description 3
- 229910052684 Cerium Inorganic materials 0.000 abstract description 2
- 229910052746 lanthanum Inorganic materials 0.000 abstract description 2
- 229910052777 Praseodymium Inorganic materials 0.000 abstract 1
- 229910052751 metal Inorganic materials 0.000 abstract 1
- 239000000047 product Substances 0.000 description 27
- 229910000831 Steel Inorganic materials 0.000 description 17
- 239000010959 steel Substances 0.000 description 17
- 239000000463 material Substances 0.000 description 7
- 238000005336 cracking Methods 0.000 description 6
- 230000003647 oxidation Effects 0.000 description 5
- 238000007254 oxidation reaction Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 4
- 238000012360 testing method Methods 0.000 description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 3
- 238000005452 bending Methods 0.000 description 3
- 229910052802 copper Inorganic materials 0.000 description 3
- 239000010949 copper Substances 0.000 description 3
- 238000011156 evaluation Methods 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000010935 stainless steel Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 229910000963 austenitic stainless steel Inorganic materials 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 238000005520 cutting process Methods 0.000 description 2
- 239000011888 foil Substances 0.000 description 2
- 238000009863 impact test Methods 0.000 description 2
- 238000002347 injection Methods 0.000 description 2
- 239000007924 injection Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000004080 punching Methods 0.000 description 2
- 230000007704 transition Effects 0.000 description 2
- 206010011224 Cough Diseases 0.000 description 1
- 229910001122 Mischmetal Inorganic materials 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000006866 deterioration Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 239000003779 heat-resistant material Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000001247 metal acetylides Chemical class 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000008707 rearrangement Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は、耐熱性あるいは耐食性に優れたフェライト系
ステンレス鋼板の製造方法に関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a method for producing a ferritic stainless steel sheet having excellent heat resistance or corrosion resistance.
〔従来の技術］
近年、耐熱性材料としてはＡＡまたはＳｉを含有するフ
ェライト系ステンレス鋼が、また耐食性材料としてＭｏ
を含有するフェライト系ステンレス鋼が注目されている
。なぜなら、このようなフェライト系ステンレス鋼は、
耐熱性においてオーステナイト系ステンレス鋼よりもは
るかに優れた耐酸化性を有し、また耐食性においてオー
ステナイト系ステンレス鋼で問題とされる応力腐食割れ
に対して強い抵抗性を示すことが明かとなってきたため
である。これらは、自動車用排ガス部品、ストーブ部品
、加熱炉々壁等に使用されている。[Prior art] In recent years, AA or Si-containing ferritic stainless steel has been used as a heat-resistant material, and Mo as a corrosion-resistant material.
Ferritic stainless steel containing . This is because such ferritic stainless steel
It has become clear that it has far superior oxidation resistance than austenitic stainless steel in terms of heat resistance, and has strong resistance to stress corrosion cracking, which is a problem with austenitic stainless steel in terms of corrosion resistance. It is. These are used for automobile exhaust gas parts, stove parts, heating furnace walls, etc.
しかしながら、Ａｊ２ 、Ｓｉ ，Ｍｏを含有したフ
ェライト系ステンレス鋼の熱延鋼帯は靭性が著しく低い
ので、室温で同調帯のコイルを展開するとき、あるいは
さらに冷間圧延するとき割れや板破断等を生じ、甚だし
いときには冷間圧延ができない場合がある。これを回避
するには、銅帯を遷移温度以上に予熱して通板すれば良
いが、予熱による工程費アップを招くほか、予熱温度が
高い場合は作業性や能率が悪く、安全上の面からも好ま
しくない。また、熱延洞帯や冷延畑帯の製品に曲げ、切
断、打ち抜き等の加工を施す場合も、割れの問題がある
。However, hot-rolled steel strips made of ferritic stainless steel containing Aj2, Si, and Mo have extremely low toughness, so cracks and plate breakage may occur when the tuning strip coil is developed at room temperature or when further cold rolled. In extreme cases, cold rolling may not be possible. To avoid this, it is possible to preheat the copper strip to a temperature higher than the transition temperature before threading it, but in addition to increasing the process cost due to preheating, high preheating temperatures impede workability and efficiency, resulting in safety concerns. I don't like it either. Furthermore, when hot-rolled sinusoidal products or cold-rolled sinusoidal products are subjected to processing such as bending, cutting, punching, etc., there is also the problem of cracking.
従って、熱延鋼書コイルの展開や冷間圧延等の製造工程
や製品加工において割れの発生しない、耐熱耐食性に優
れたフェライ１・系ステンレス鋼板の製造方法が強く要
望されていた。Therefore, there has been a strong demand for a method for producing Ferrai 1 stainless steel sheets that have excellent heat and corrosion resistance and do not cause cracks during production processes such as hot-rolled steel coil development and cold rolling, and during product processing.
このようなＡｆｆ ，Ｓｉ ，Ｍｏ含有フェライト系
ステンレス鋼熱延銅帯の脆化現象を防止するための従来
技術としては、例えば特開昭６０−２２８１６号公報に
開示されているように、Ｃ，Ｎを低減し熱間圧延後に１
０℃／ｓｅｃ以上の冷却速度で急冷して４５０℃以下の
低温で巻取る方法がある。しかしながら、現状の熱間圧
延設備では注水により急冷処理を行うが、４５０℃以下
の低温巻取りを行うと注水量が多くなり板形状が悪く巻
取りが困難となる。As a conventional technique for preventing such embrittlement of ferritic stainless steel hot-rolled copper strips containing Aff, Si, and Mo, for example, as disclosed in Japanese Patent Application Laid-Open No. 60-22816, C, 1 after hot rolling by reducing N
There is a method of rapidly cooling at a cooling rate of 0°C/sec or more and winding at a low temperature of 450°C or less. However, in the current hot rolling equipment, quenching treatment is carried out by water injection, but when winding is performed at a low temperature of 450° C. or lower, the amount of water injection becomes large, and the plate shape becomes poor and winding becomes difficult.
従って、巻取りを容易にするため銅帯トップ部は無注水
にし、冷間圧延前に咳部を切捨てスクラップとしている
ので、製造歩留の点で問題がある。Therefore, in order to facilitate winding, water is not poured into the top part of the copper strip, and the cough part is cut off and scrapped before cold rolling, which poses a problem in terms of manufacturing yield.
本発明は、Ａ／ ，Ｓｉ ．Ｍｏを含有する耐熱耐食
性に優れたフェライト系ステンレス鋼板の靭性を改善す
ることによって、製造歩留を向上させ、作業性を改善し
、さらに製品の加工性を向上させることを目的としてい
る。The present invention provides A/, Si. The aim is to improve the manufacturing yield, improve workability, and further improve the workability of products by improving the toughness of ferritic stainless steel sheets that contain Mo and have excellent heat and corrosion resistance.
本発明は、この目的のために製造工程およびその条件を
検討した結果、完威したもので、その要旨とするところ
は下記のとおりである。The present invention was achieved as a result of studying the manufacturing process and its conditions for this purpose, and the gist thereof is as follows.
（１）重量％にて、Ｃ ： ０．０２％以下、Ｎ ：
０．０２％以下、ただしＣ（％）＋Ｎ（％）：０．０３
％以下、Ｃｒ ： １０．０〜４０．０％と、Ａｆｆ
ｉ ， Ｓｉ ， Ｍｏから選ばれる元素の１種ま
たは２種以上：合計１． ０〜５．０％と、希土類金属
元素（ＲＥＭ） ：合計０．０１〜０．５０％とを含
有し、熱間圧延温度域でフェライト単相の組織を有する
フェライト系ステンレス鋼のスラブを、圧下率を８０％
以上として熱間圧延した後２５℃／ｓｅｃ以上の冷却速
度で冷却し、４５０超〜６００℃以下で巻取り、熱延製
品とすることを特徴とする耐熱耐食性に優れたフェライ
ト系ステンレス鋼板の製造方法。(1) In weight%, C: 0.02% or less, N:
0.02% or less, however, C (%) + N (%): 0.03
% or less, Cr: 10.0 to 40.0%, Af
One or more elements selected from i, Si, Mo: total 1. A slab of ferritic stainless steel containing 0 to 5.0% and a total of 0.01 to 0.50% of rare earth metal elements (REM) and having a ferritic single phase structure in the hot rolling temperature range, Reduce the reduction rate to 80%
Production of a ferritic stainless steel sheet with excellent heat and corrosion resistance characterized by hot rolling the above, cooling at a cooling rate of 25°C/sec or more, and winding at a temperature of over 450°C to 600°C or less to obtain a hot rolled product. Method.
（２）泊ｔ？ｉ＃（１）に記載したフェライト系ステン
レス鋼の熱延製品に、圧下率をｌＯ％以上とする冷間圧
延を行って冷延製品とすることを特徴とする耐熱耐食性
に優れたフェライト系ステンレス鋼板の製造方法。(2) Stay overnight? A ferritic stainless steel with excellent heat and corrosion resistance, which is obtained by cold rolling a hot-rolled ferritic stainless steel product described in i#(1) with a rolling reduction of 1O% or more. Method of manufacturing steel plates.
（３）前記番（１）に記載したフェライト系ステンレス
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延と
、８５０〜１１００℃の温度域で焼鈍し８００〜６００
℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱処
理とを１回または２回以上行って冷延製品とすることを
特徴とする耐熱耐食性に優れたフェライト系ステンレス
鋼板の製漬方法。(3) The hot-rolled ferritic stainless steel product described in item (1) above is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 600°C.
A method for manufacturing a ferritic stainless steel sheet having excellent heat and corrosion resistance, the method comprising performing a heat treatment of cooling the steel sheet between 0.degree. and 25.degree. C. at a cooling rate of 25.degree.
（４）前ｔ己填（１）に記載したフェライト系ステンレ
ス鋼の熱延製品に、圧下率を１０％以上とする冷間圧延
と、８５０〜１１００℃の温度域で焼鈍し８００〜６０
０℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱
処理とを１回または２回以上行い、ついで圧下率を１０
％以上とする冷間圧延を行って冷延製品とすることを特
徴とする耐熱耐食性に優れたフェライト系ステンレス鋼
板の製造方法。(4) The hot-rolled ferritic stainless steel product described in (1) above is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 60°C.
A heat treatment of cooling between 0°C and a cooling rate of 25°C/sec or more is performed once or twice, and then the rolling reduction rate is reduced to 10°C.
% or more to obtain a cold-rolled product.
（５）重量％にて、Ｃ ： ０．０２％以下、Ｎ ：
０．０２％以下、ただしＣ（％）＋Ｎ（％）：０．０３
％以下、Ｃｒ ： １０．０〜４０．０％と、Ａｆ
，Ｓｉ ，Ｍｏから選ばれる元素の１種または２種
以上二合計１．０〜５．０％と、希土類金属元素（ＲＥ
Ｍ） ：合計０．０１〜０．５０％と、Ｔｉ ，Ｎ
ｂ ，Ｖ，Ｚｒ ，Ｔａ ，Ｈｆ ，Ｂから選
ばれる元素の１種または２種以上：合計０．００５〜０
．５０％とを含有し、熱間圧延温度域でフェライト単相
の組織を有するフェライト系ステンレス鋼のスラブを、
圧下率を８０％以上として熱間圧延した後２５℃／ｓｅ
ｃ以上の冷却速度で冷却し、４５０超〜６００℃以下で
巻取り、熱延製品とすることを特徴とする耐熱耐食性に
優れたフェライト系ステンレス鋼板の製造方法。(5) In weight%, C: 0.02% or less, N:
0.02% or less, however, C (%) + N (%): 0.03
% or less, Cr: 10.0 to 40.0%, Af
, Si, Mo, and a total of 1.0 to 5.0% of one or more elements selected from , Si, Mo, and rare earth metal elements (RE
M): total 0.01-0.50%, Ti, N
One or more elements selected from b, V, Zr, Ta, Hf, and B: total 0.005 to 0
．． A slab of ferritic stainless steel containing 50% and having a single ferritic phase structure in the hot rolling temperature range,
25℃/se after hot rolling with a reduction rate of 80% or more
1. A method for producing a ferritic stainless steel sheet with excellent heat and corrosion resistance, which comprises cooling at a cooling rate of at least c.
（ ６ ） ＠垢呑（ ５ ）に記載したフェライト系
ステンレス鋼の熱延製品に、圧下率を１０％以上とする
冷間圧延を行って冷延製品とすることを特徴とする耐熱
耐食性に優れたフェライト系ステンレス鋼板の製造方法
。(6) A cold-rolled product with excellent heat and corrosion resistance characterized by cold-rolling the ferritic stainless steel hot-rolled product described in (5) at a rolling reduction of 10% or more. A method for producing ferritic stainless steel sheets.
（ ７ ） 前把＃（ ５ ）に記載したフェライト系
ステンレス鋼の熱延製品に、圧下率を１０％以上とする
、冷間圧延と、８５０〜１１００℃の温度域で焼鈍し８
００〜６００℃の間を２５℃／ｓｅｃ以上の冷却速度で
冷却する熱処理とを１回または２回以上行って冷延製品
とすることを特徴とする耐熱耐食性に優れたフェライト
系ステンレス鋼板の製造方法。(7) The hot-rolled ferritic stainless steel product described in Preamble #(5) is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C.
Production of a ferritic stainless steel sheet with excellent heat and corrosion resistance, characterized in that it is made into a cold-rolled product by performing heat treatment of cooling between 00 and 600 °C at a cooling rate of 25 °C / sec or more once or twice or more. Method.
（８ ） Ｉｉ′ＩｊＥ！（５ ）に記載したフェライ
ト系ステンレス鋼の熱延製品に、圧下率を１０％以上と
する冷間圧延と、８５０〜１１００℃の温度域で焼鈍し
８００〜６００℃の間を２５℃：／ｓｅｃ以上の冷却速
度で冷却する熱処理とを１回または２回以上行い、つい
で圧下率を１０％以上とする冷間圧延を行って冷延製品
とすることを特徴とする耐熱耐食性に優れたフェライト
系ステンレス鋼板の製造方法。(8) Ii′IjE! The hot-rolled ferritic stainless steel product described in (5) is cold-rolled with a rolling reduction of 10% or more, annealed in a temperature range of 850-1100°C, and then heated at 25°C between 800-600°C. A ferrite with excellent heat and corrosion resistance characterized by being subjected to heat treatment of cooling at a cooling rate of sec or more once or twice or more, and then cold rolling with a rolling reduction of 10% or more to obtain a cold-rolled product. A method for manufacturing stainless steel sheets.
〔作 用］
本発明の限定理由を以下に詳細に説明する。尚、本発明
におけるスラブとは、連続鋳造鋳片、これにブレイクダ
ウンを行った鋳片、インゴット鋳片とこれに分塊圧延を
行った鋼片である。[Function] The reasons for the limitations of the present invention will be explained in detail below. Incidentally, the slab in the present invention refers to a continuously cast slab, a slab that has been subjected to breakdown, an ingot slab, and a steel slab that has been subjected to blooming rolling.
請求項（１）〜（４）における戒分の限定理由はつぎの
とおりである。The reasons for limiting the precepts in claims (1) to (4) are as follows.
Ｃ，Ｎは、それぞれが０．０２％を超えて存在する場合
もしくはＣ＋Ｎで０．０３％を超える場合、熱延鋼帯の
靭性を著しく低下させる。従って、Ｃ，Ｈの戒分範囲は
、それぞれ０．０２％以下でかつＣ＋Ｈの総量が０．０
３％以下とした。When each of C and N exceeds 0.02%, or when C+N exceeds 0.03%, the toughness of the hot rolled steel strip is significantly reduced. Therefore, the precept range for C and H is 0.02% or less, and the total amount of C+H is 0.0%.
It was set to 3% or less.
Ｃｒはステンレス鋼の耐酸化性および耐食性を確保する
最も基本的な元素である。本発明においては、１０％未
満ではこれらの特性が十分に確保されず、一方４０％を
超えて含有すると特に熱延鋼帯の靭性および冷間での加
工性（延性）が著しく低下する。従って、Ｃｒの戒分範
囲は１０．０〜４０。０％とした。Cr is the most fundamental element that ensures the oxidation resistance and corrosion resistance of stainless steel. In the present invention, if the content is less than 10%, these properties cannot be sufficiently ensured, while if the content exceeds 40%, the toughness and cold workability (ductility) of the hot-rolled steel strip will be significantly reduced. Therefore, the Cr content range was set to 10.0 to 40.0%.
ＡｌおよびＳｔ は、フェライト系ステンレス鋼の耐酸
化性を向上させる元素であり、ＭＯは耐食性を向上させ
る元素である。本発明においては、これら３元素のうち
から所望の特性に応じて１種または２種以上を含有させ
る。合計で１．０％未満では耐酸化性あるいは耐食性を
向上させるのに十分でなく、５．０％を超えて含有する
と特に熱延鋼帯の靭性および冷間での加工性を低下する
。従って、Ａｊ！ ，Ｓｉ ，Ｍｏの戒分範囲は合計
で１．０〜５． ０％とした。Al and St are elements that improve the oxidation resistance of ferritic stainless steel, and MO is an element that improves the corrosion resistance. In the present invention, one or more of these three elements is contained depending on desired characteristics. If the total content is less than 1.0%, it is not sufficient to improve oxidation resistance or corrosion resistance, and if the content exceeds 5.0%, the toughness and cold workability of the hot-rolled steel strip will be particularly reduced. Therefore, Aj! , Si, and Mo have a total range of 1.0 to 5. It was set to 0%.
希土類金属元素（ＲＥＭ）は、Ｌａ ，Ｃｅ ，Ｐ
ｒ ，Ｎｄ等のランタノイドのことであり、耐酸化性
を顕著に向上させるために添加し、この効果は０．０１
％未満では十分でない。しかしながら、０．５０％を超
えて添加すると、ＲＥＭ系酸化物が粗大化するため、熱
間加工性が著しく低下し熱間圧延にて割れが発生する。Rare earth metal elements (REM) include La, Ce, P
Lanthanoids such as r, Nd, etc. are added to significantly improve oxidation resistance, and this effect is 0.01
Less than % is not sufficient. However, if it is added in an amount exceeding 0.50%, the REM-based oxide becomes coarse, resulting in significantly reduced hot workability and cracking during hot rolling.
従って、ＲＥＭの成分範囲は合計で０．０１〜０．５０
％とした。Therefore, the total component range of REM is 0.01 to 0.50
%.
請求項（５）〜（８）は、上記戒分のほか、さらにＴｉ
，Ｎｂ ，Ｖ，Ｚｒ ，Ｔａ ，Ｈｆ ，
Ｂから選ばれる元素の１種または２種以上を含有する。Claims (5) to (8) further include Ti in addition to the above precepts.
, Nb, V, Zr, Ta, Hf,
Contains one or more elements selected from B.
これらの元素は、それぞれが窒化物あるいは炭化物を形
威して固溶Ｃ，Ｎを減少させるとともに熱間圧延中の大
圧下加工により導入される転位上に析出して組織を微細
化させ、熱延鋼帯の靭性を一層向上させる。この効果は
、１種または２種以上合計でｏ． ｏｏｓ％未満では十
分でな＜ 、０．５０％を超えて含有すると冷間での加
工性を著しく劣化させる。従って、Ｔｉ ，Ｎｂ
，Ｖ，Ｚｒ ，Ｔａ ，ＨｆＢの成分範囲は、合計
でｏ．ｏｏｓ〜０．５０％とした。Each of these elements forms nitrides or carbides to reduce solid solution C and N, and also precipitates on dislocations introduced by large reduction during hot rolling, making the structure finer and reducing heat resistance. Further improve the toughness of rolled steel strip. This effect is caused by one or more types of o. If it is less than 0.0s%, it is not sufficient, and if it is more than 0.50%, the cold workability will be significantly deteriorated. Therefore, Ti, Nb
, V, Zr , Ta , and HfB, the total range of components is o. oos to 0.50%.
本発明におけるフェライト系ステンレス鋼は、熱間圧延
温度域でフェライト単相となるように成分調整する。熱
間圧延温度でオーステナイト相が析出すると、熱間圧延
終了後の急速冷却によりマルテンサイト相に変態しごク
ロラックの発生核となり靭性を劣化させるからである。The composition of the ferritic stainless steel in the present invention is adjusted so that it becomes a single ferrite phase in the hot rolling temperature range. This is because when the austenite phase precipitates at the hot rolling temperature, it transforms into the martensitic phase due to rapid cooling after hot rolling, becomes a nucleus for the generation of iron chlorac, and deteriorates toughness.
熱間圧延温度は、１２５０〜８５０℃とするのが好まし
い。The hot rolling temperature is preferably 1250 to 850°C.
請求項（１）および（５）は、上記戒分のフェライト系
ステンレス鋼スラブを熱間圧延して熱延製品とする。本
発明者等は、熱延鋼帯の靭性に及ぼすＲＥＭｆｆｉと熱
間圧延条件の影響を検討した結果、ＲＥＭＩを合計で０
．０１％以上含有した場合、熱間圧延の圧下率を８０％
以上の大圧下とし、かつ熱間圧延終了後２５℃／ｓｅｃ
以上の冷却速度で６００℃以下に急冷すると、靭性が顕
著に改善されることを見い出した。この靭性改善の機構
は現在まだ詳細には明らかにされていないが、均一に微
細分散したＲＥＭ系酸化物の周りに熱間圧延の大圧下に
より導入された転位が高密度に集積し、熱間圧延終了時
までの転位の再配列により微細なサブダレインが形威さ
れるためと考えられる。この組織は、その後の急冷によ
り凍結され、常温まで維持されるため、組織微細化によ
り靭性が著しく改善されるものと推測される。従って、
熱間圧延の圧下率は、８０％以上とした。さらに靭性を
向上させるためには、９０％以上とするのが好ましい。Claims (1) and (5) provide hot-rolling of the above-mentioned ferritic stainless steel slab to produce a hot-rolled product. The present inventors investigated the effects of REMffi and hot rolling conditions on the toughness of hot rolled steel strips, and found that REMI was 0 in total.
．． If the content is 0.1% or more, the reduction rate of hot rolling is 80%.
A large reduction of 25°C/sec after hot rolling.
It has been found that when the material is rapidly cooled to 600° C. or less at the above cooling rate, the toughness is significantly improved. The mechanism of this toughness improvement has not yet been clarified in detail, but dislocations introduced by the large reduction during hot rolling accumulate around the uniformly finely dispersed REM oxide, resulting in This is thought to be due to the formation of fine subdalen due to the rearrangement of dislocations until the end of rolling. Since this structure is then frozen by rapid cooling and maintained at room temperature, it is presumed that the toughness is significantly improved by the microstructure. Therefore,
The reduction ratio of hot rolling was 80% or more. In order to further improve toughness, it is preferably 90% or more.
また、熱間圧延終了後の冷却速度は、２５℃／ｓｅｃ以
上とし、巻取り温度まで急冷する。冷却温度が２５℃／
ｓｅｃ未満だとσ相や金属間化合物等の脆化相が析出し
易いため、熱延材の靭性を劣化させるとともに、熱間圧
延終了時の微細なサブグレイン組織を凍結することがで
きないからである。Further, the cooling rate after hot rolling is set to 25° C./sec or more, and the material is rapidly cooled to the coiling temperature. Cooling temperature is 25℃/
If it is less than sec, brittle phases such as σ phase and intermetallic compounds are likely to precipitate, which deteriorates the toughness of the hot rolled material and makes it impossible to freeze the fine subgrain structure at the end of hot rolling. be.
巻取り温度は４５０超〜６００℃以下とする。６００℃
より高いと、熱延終了後の冷却速度が２５℃／ｓｅｃ以
上であったとしても、巻取り後の徐冷中の熱サイクルに
よりσ相や金属間化合物等の脆化相が析出し易いため、
熱延材の靭性を劣化させる。また、前述したように、４
５０℃以下では注水量が多くなり板形状が悪く巻取りが
困難となる。The winding temperature is from more than 450°C to 600°C or less. 600℃
If it is higher, even if the cooling rate after hot rolling is 25°C/sec or more, brittle phases such as σ phase and intermetallic compounds are likely to precipitate due to thermal cycles during slow cooling after coiling.
Deteriorates the toughness of hot-rolled materials. Also, as mentioned above, 4
If the temperature is below 50°C, the amount of water injected will be large, resulting in poor plate shape and difficulty in winding.
請求項（１）および（５）における熱延製品は、熱延ま
までも良いが、特に強加工を行う用途には必要に応じて
焼鈍しても良い。好ましい焼鈍条件としては、靭性確保
の点から焼鈍温度が８５０〜ｌ１００℃で冷却速度が８
００ 〜６００℃の間で２５℃／ｓｅｃ以上である。The hot-rolled products according to claims (1) and (5) may be hot-rolled as is, but may be annealed if necessary especially in applications where heavy working is performed. From the viewpoint of ensuring toughness, preferable annealing conditions include an annealing temperature of 850 to 100°C and a cooling rate of 8.
It is 25°C/sec or more between 00°C and 600°C.
請求項（２）および（６）は、請求項（１）および（５
）で得られた熱延製品に冷間圧延を行って冷延製品とす
る。尚、用いる熱延製品は、熱延ままでも良く、冷間圧
延の圧下率が大きい場合には必要に応じて冷延前に焼鈍
しても良い。この場合の好ましい焼鈍条件としては、後
述するように靭性確保の点から温度が８５０〜１１００
℃で冷却速度が８００〜６００℃の間で２５℃／ｓｅｃ
である。Claims (2) and (6) are defined as claims (1) and (5).
) is subjected to cold rolling to obtain a cold rolled product. Note that the hot-rolled product to be used may be as hot-rolled, or may be annealed before cold-rolling if necessary if the rolling reduction of the cold-rolling is large. In this case, preferable annealing conditions include a temperature of 850 to 1100 from the viewpoint of ensuring toughness, as described later.
℃ and the cooling rate is 25℃/sec between 800 and 600℃
It is.
冷間圧延の圧下率は、１０％より小さいと、転位が粒界
や析出物等へ不均一に導入されるため、これらの場所に
おける応力集中が助長されミクロクラックが容易に発生
・伝播し、靭性が劣化する。If the rolling reduction ratio in cold rolling is less than 10%, dislocations will be introduced unevenly into grain boundaries and precipitates, which will promote stress concentration in these places and cause microcracks to easily generate and propagate. Toughness deteriorates.
しかしながら、１０％以上の冷間圧延を行うと転位がマ
トリンクスにほぼ均一にかつ高密度に導入され、このよ
うな転位領域は逆にミクロクランクの伝播抵抗となるた
め、延性脆性遷移温度が下がり靭性が向上する。従って
、冷間圧延の圧下率の範囲を１０％以上とした。さらに
靭性を向上させるためには、３０％以上とするのが好ま
しい。However, when cold rolling of 10% or more is performed, dislocations are introduced almost uniformly and densely into the matrix, and such dislocation regions conversely act as a propagation resistance of the microcrank, lowering the ductile-brittle transition temperature and increasing the toughness. will improve. Therefore, the range of the reduction ratio in cold rolling was set to 10% or more. In order to further improve toughness, it is preferably 30% or more.
請求項（３）および（７）は、請求項（１）および（５
）で得られた熱延製品に冷間圧延と熱処理を行って冷延
製品とする。冷間圧延と熱処理は、製品の板厚に応じて
２回以上行ってもよい。冷間圧延の圧下率は上記理由に
より１０％以上とした。Claims (3) and (7) are defined as claims (1) and (5).
) is subjected to cold rolling and heat treatment to obtain a cold rolled product. Cold rolling and heat treatment may be performed two or more times depending on the thickness of the product. The rolling reduction ratio of cold rolling was set to 10% or more for the above reason.
熱処理における焼鈍温度は、８５０℃より低いと再結晶
が十分でなく、一方、１１００℃を超えると結晶粒が粗
大化し靭性が著しく劣化する。従って、焼鈍温度の範囲
を８５０〜１１００”Ｃとした。If the annealing temperature in the heat treatment is lower than 850°C, recrystallization will not be sufficient, while if it exceeds 1100°C, the crystal grains will become coarse and the toughness will deteriorate significantly. Therefore, the annealing temperature range was set to 850-1100''C.
焼鈍後の冷却速度は、８００〜６００℃の間で２５℃／
ｓｅｃ未満とするとび相や金属間化合物等の脆化相がこ
の温度範囲で析出し易いため、冷延材の靭性を劣化させ
る。従って、焼鈍後の冷却速度は、８００〜６００℃の
間で２５℃／ｓｅｃ以上とした。The cooling rate after annealing is 25℃/25℃ between 800 and 600℃.
If it is less than sec, brittle phases such as elongated phases and intermetallic compounds are likely to precipitate in this temperature range, resulting in deterioration of the toughness of the cold rolled material. Therefore, the cooling rate after annealing was set to 25°C/sec or more between 800 and 600°C.
請求項（４）および（８）は、請求項（１）および（５
）で得られた熱延製品に冷間圧延と熱処理を１回または
２回以上行い、さらに冷間圧延を行って冷延製品とする
。冷間圧延の圧下率は上記理由により１０％以上とし、
熱処理の温度および冷却速度も上記理由により８５０−
１１００℃の温度域で焼鈍したのち８００〜６００℃の
間を２５゜［：／ｓｅｃ以上の冷却速度で冷却すること
とした。Claims (4) and (8) are defined as claims (1) and (5).
The hot-rolled product obtained in ) is subjected to cold rolling and heat treatment once or twice or more, and further cold-rolled to obtain a cold-rolled product. The reduction rate of cold rolling is set to 10% or more for the above reasons,
The heat treatment temperature and cooling rate are also 850-
After annealing in a temperature range of 1100°C, cooling was performed between 800 and 600°C at a cooling rate of 25°/sec or more.
請求項（２）．（４），（６）および（８）における冷
延製品は、高強度が要求される場合、または極薄板ある
いは箔として使われる場合に使用され、請求項（３）お
よび（７）における冷延製品は、加工性が要求される場
合に使用される。Claim (2). The cold-rolled products in (4), (6) and (8) are used when high strength is required or when used as ultra-thin plates or foils, and the cold-rolled products in claims (3) and (7) The product is used when processability is required.
〔実施例］
（１）転炉−ＶＯＤ法あるいは真空溶解法により第１表
に示すフェライト系ステンレス鋼を溶製した。ＲＥＭは
、鋳造直前にミッシュメタルワイヤーにて添加した。こ
れらの鋼を第２表に示される条件に従って製造し板厚：
３．５〜６． ０ ｍｍの熱延鋼帯とした。靭性評価は
、ＪＩＳ規定に準拠したサブサイズ（厚み：３，３＋ｎ
ｍ）のＶノッチシャルピー試験片を圧延方向と平行に採
取し衝撃試験を行い、衝撃値が２Ｋｇｍ／ｃ＋Ｊになる
温度（ＶＴ２ ： ℃ ）で評価した。ｖＴ，が２０℃
以下である場合、予熱せずに熱延鋼帯の冷間圧延が可能
である。２０℃を超えた場合には、予熱せずに冷間圧延
を行うと、衝撃等による板破断の危険性が極めて高くな
る。[Example] (1) Ferritic stainless steels shown in Table 1 were melted using a converter-VOD method or a vacuum melting method. REM was added via misch metal wire just before casting. These steels were manufactured according to the conditions shown in Table 2, and the plate thickness:
3.5-6. It was made into a 0 mm hot rolled steel strip. Toughness evaluation is based on sub-size (thickness: 3,3+n
A V-notch Charpy test piece of m) was sampled parallel to the rolling direction and subjected to an impact test, and evaluated at a temperature (VT2: °C) at which the impact value was 2 Kgm/c+J. vT, is 20℃
If it is below, the hot rolled steel strip can be cold rolled without preheating. If the temperature exceeds 20° C. and cold rolling is performed without preheating, the risk of plate breakage due to impact or the like becomes extremely high.
本発明法により製造した熱延鋼帯は、靭性が大いに改善
されており、冷間圧延時に板破断等のトラブルが発生し
ないことがわかる．
（２）転炉−ＶＯＤ法あるいは真空溶解法により溶製し
熱延鋼帯とした。第ｌ表に示される本発明対象材を第３
表に示される条件に従って熱処理あるいは冷間圧延した
。靭性評価は、板厚が３．３閣を超えるものについてＪ
ＩＳ規格に準拠したサブサイズ（厚み：３．３ｍｍ）の
Ｖノッチシャルピー試験片を圧延方向と平行に採取し、
板厚が３．３帥以下１． ５ ｏｎｎ以上について板厚
のままのＶノッチシャルピー試験片を圧延方向と平行に
採取し衝撃試験を行い、ｖＴ．で評価した。板厚が１．
５ ｍｍ未満のものは、２ｔ．（ｔ：板厚）密着曲げ
試験により割れが発生する温度で評価した。It can be seen that the hot-rolled steel strip produced by the method of the present invention has greatly improved toughness and does not suffer from problems such as plate breakage during cold rolling. (2) A hot-rolled steel strip was produced by converter-VOD method or vacuum melting method. The material subject to the present invention shown in Table 1 was
Heat treatment or cold rolling was performed according to the conditions shown in the table. Toughness evaluation is J for plates with a thickness exceeding 3.3 mm.
A sub-sized (thickness: 3.3 mm) V-notch Charpy test piece compliant with IS standards was taken parallel to the rolling direction,
Plate thickness is 3.3 mm or less1. 5 onn or more, a V-notch Charpy test piece with the same plate thickness was taken parallel to the rolling direction and subjected to an impact test. It was evaluated by The plate thickness is 1.
For those less than 5 mm, 2t. (t: plate thickness) Evaluation was made at the temperature at which cracking occurs in a close contact bending test.
本発明法により製造した冷延鋼帯は、靭性が大いに改善
されており、冷間圧延時に板破断等のトラブルが発生せ
ず、極薄板、箔まで製造することができることがわかる
。It can be seen that the cold-rolled steel strip produced by the method of the present invention has greatly improved toughness, and troubles such as plate breakage do not occur during cold rolling, and even ultra-thin plates and foils can be produced.
以上のことから明らかな如く、本発明法に従いＡ！！，
Ｓｉ ，Ｍｏを含有する耐熱耐食性に優れたフェライ
ト系ステンレス鋼板を製造すれば、熱延鋼帯や冷延鋼帯
の冷間圧延時に割れや板破断を防止し、これら鋼帯を製
品として使用するに際して、曲げ、切断、打ち抜き等を
施す場合、割れ発生を解消し、製造歩留および作業性が
大幅に改善される。As is clear from the above, according to the method of the present invention, A! ! ，
If we manufacture ferritic stainless steel sheets containing Si and Mo that have excellent heat and corrosion resistance, we can prevent cracking and plate breakage during cold rolling of hot-rolled steel strips and cold-rolled steel strips, and use these steel strips as products. During bending, cutting, punching, etc., cracking is eliminated, and manufacturing yield and workability are significantly improved.
Claims (8)
％以下、ただしＣ（％）＋Ｎ（％）：０．０３％以下、
Ｃｒ：１０．０〜４０．０％と、Ａｌ、Ｓｉ、Ｍｏから
選ばれる元素の１種または２種以上：合計１．０〜５．
０％と、希土類金属元素（ＲＥＭ）：合計０．０１〜０
．５０％とを含有し、熱間圧延温度域でフェライト単相
の組織を有するフェライト系ステンレス鋼のスラブを、
圧下率を８０％以上として熱間圧延した後２５℃／ｓｅ
ｃ以上の冷却速度で冷却し、４５０超〜６００℃以下で
巻取り、熱延製品とすることを特徴とする耐熱耐食性に
優れたフェライト系ステンレス鋼板の製造方法。(1) In weight%, C: 0.02% or less, N: 0.02
% or less, however, C (%) + N (%): 0.03% or less,
Cr: 10.0-40.0% and one or more elements selected from Al, Si, and Mo: total 1.0-5.
0% and rare earth metal elements (REM): total 0.01-0
．． A slab of ferritic stainless steel containing 50% and having a single ferritic phase structure in the hot rolling temperature range,
25℃/se after hot rolling with a reduction rate of 80% or more
1. A method for producing a ferritic stainless steel sheet with excellent heat and corrosion resistance, which comprises cooling at a cooling rate of at least c.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延を
行って冷延製品とすることを特徴とする耐熱耐食性に優
れたフェライト系ステンレス鋼板の製造方法。(2) A cold-rolled product with excellent heat and corrosion resistance, characterized in that the hot-rolled product of ferritic stainless steel according to claim (1) is cold-rolled at a rolling reduction of 10% or more. A method for manufacturing ferritic stainless steel sheets.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延と
、８５０〜１１００℃の温度域で焼鈍し８００〜６００
℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱処
理とを１回または２回以上行って冷延製品とすることを
特徴とする耐熱耐食性に優れたフェライト系ステンレス
鋼板の製造方法。(3) The hot rolled product of ferritic stainless steel according to claim (1) is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 600°C.
A method for producing a ferritic stainless steel sheet having excellent heat and corrosion resistance, which comprises performing heat treatment at a cooling rate of 25° C./sec or more once or twice or more to obtain a cold-rolled product.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延と
、８５０〜１１００℃の温度域で焼鈍し８００〜６００
℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱処
理とを１回または２回以上行い、ついで圧下率を１０％
以上とする冷間圧延を行って冷延製品とすることを特徴
とする耐熱耐食性に優れたフェライト系ステンレス鋼板
の製造方法。(4) The hot-rolled product of ferritic stainless steel according to claim (1) is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 600°C.
℃ at a cooling rate of 25℃/sec or more is performed once or twice or more, and then the rolling reduction rate is 10%.
A method for manufacturing a ferritic stainless steel sheet with excellent heat and corrosion resistance, which comprises performing the above cold rolling to obtain a cold rolled product.
％以下、ただしＣ（％）＋Ｎ（％）：０．０３％以下、
Ｃｒ：１０．０〜４０．０％と、Ａｌ、Ｓｉ、Ｍｏから
選ばれる元素の１種または２種以上：合計１．０〜５．
０％と、希土類金属元素（ＲＥＭ）：合計０．０１〜０
．５０％と、Ｔｉ、Ｎｂ、Ｖ、Ｚｒ、Ｔａ、Ｈｆ、Ｂか
ら選ばれる元素の１種または２種以上：合計０．００５
〜０．５０％とを含有し、熱間圧延温度域でフェライト
単相の組織を有するフェライト系ステンレス鋼のスラブ
を、圧下率を８０％以上として熱間圧延した後２５℃／
ｓｅｃ以上の冷却速度で冷却し、４５０超〜６００℃以
下で巻取り、熱延製品とすることを特徴とする耐熱耐食
性に優れたフェライト系ステンレス鋼板の製造方法。(5) In weight%, C: 0.02% or less, N: 0.02
% or less, however, C (%) + N (%): 0.03% or less,
Cr: 10.0-40.0% and one or more elements selected from Al, Si, and Mo: total 1.0-5.
0% and rare earth metal elements (REM): total 0.01-0
．． 50% and one or more elements selected from Ti, Nb, V, Zr, Ta, Hf, and B: total 0.005
A slab of ferritic stainless steel containing ~0.50% and having a ferritic single phase structure in the hot rolling temperature range is hot rolled at a rolling reduction of 80% or more and then rolled at 25°C/
1. A method for producing a ferritic stainless steel sheet having excellent heat and corrosion resistance, which comprises cooling at a cooling rate of sec or more and winding at a temperature of more than 450° C. to less than 600° C. to obtain a hot-rolled product.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延を
行って冷延製品とすることを特徴とする耐熱耐食性に優
れたフェライト系ステンレス鋼板の製造方法。(6) A cold-rolled product with excellent heat and corrosion resistance, characterized in that the hot-rolled product of ferritic stainless steel according to claim (5) is cold-rolled at a rolling reduction of 10% or more. A method for manufacturing ferritic stainless steel sheets.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延と
、８５０〜１１００℃の温度域で焼鈍し８００〜６００
℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱処
理とを１回または２回以上行って冷延製品とすることを
特徴とする耐熱耐食性に優れたフェライト系ステンレス
鋼板の製造方法。(7) The hot rolled product of ferritic stainless steel according to claim (5) is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 600°C.
A method for producing a ferritic stainless steel sheet having excellent heat and corrosion resistance, which comprises performing heat treatment at a cooling rate of 25° C./sec or more once or twice or more to obtain a cold-rolled product.
鋼の熱延製品に、圧下率を１０％以上とする冷間圧延と
、８５０〜１１００℃の温度域で焼鈍し８００〜６００
℃の間を２５℃／ｓｅｃ以上の冷却速度で冷却する熱処
理とを１回または２回以上行い、ついで圧下率は１０％
以上とする冷間圧延を行って冷延製品とすることを特徴
とする耐熱耐食性に優れたフェライト系ステンレス鋼板
の製造方法。(8) The hot rolled product of ferritic stainless steel according to claim (5) is subjected to cold rolling with a rolling reduction of 10% or more and annealing in a temperature range of 850 to 1100°C to a temperature of 800 to 600°C.
℃ at a cooling rate of 25℃/sec or more, and then heat treatment is performed once or twice, and then the reduction rate is 10%.
A method for manufacturing a ferritic stainless steel sheet with excellent heat and corrosion resistance, which comprises performing the above cold rolling to obtain a cold rolled product.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP18601389A JP2763141B2 (en) | 1989-07-20 | 1989-07-20 | Manufacturing method of ferritic stainless steel sheet with excellent heat and corrosion resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP18601389A JP2763141B2 (en) | 1989-07-20 | 1989-07-20 | Manufacturing method of ferritic stainless steel sheet with excellent heat and corrosion resistance |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0353026A true JPH0353026A (en) | 1991-03-07 |
| JP2763141B2 JP2763141B2 (en) | 1998-06-11 |
Family
ID=16180856
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP18601389A Expired - Lifetime JP2763141B2 (en) | 1989-07-20 | 1989-07-20 | Manufacturing method of ferritic stainless steel sheet with excellent heat and corrosion resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2763141B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012111391A1 (en) * | 2011-02-17 | 2012-08-23 | 新日鐵住金ステンレス株式会社 | High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same |
| JP2012172161A (en) * | 2011-02-17 | 2012-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and method for manufacturing the same |
| JP2012172160A (en) * | 2011-02-17 | 2012-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and method for manufacturing the same |
| GB2549729A (en) * | 2016-04-26 | 2017-11-01 | Skf Magnetic Mechatronics | Method of manufacturing a lamination stack for use in an electrical machine |
| CN114410944A (en) * | 2021-12-24 | 2022-04-29 | 苏州钢特威钢管有限公司 | Manufacturing process method for preventing super ferrite stainless steel pipe from cold rolling cracking |
-
1989
- 1989-07-20 JP JP18601389A patent/JP2763141B2/en not_active Expired - Lifetime
Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012111391A1 (en) * | 2011-02-17 | 2012-08-23 | 新日鐵住金ステンレス株式会社 | High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same |
| JP2012172161A (en) * | 2011-02-17 | 2012-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and method for manufacturing the same |
| JP2012172160A (en) * | 2011-02-17 | 2012-09-10 | Nippon Steel & Sumikin Stainless Steel Corp | High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and method for manufacturing the same |
| CN103403205A (en) * | 2011-02-17 | 2013-11-20 | 新日铁住金不锈钢株式会社 | High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same |
| EP2677055A1 (en) * | 2011-02-17 | 2013-12-25 | Nippon Steel & Sumikin Stainless Steel Corporation | High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same |
| EP2677055A4 (en) * | 2011-02-17 | 2014-11-19 | Nippon Steel & Sumikin Sst | High-purity ferritic stainless steel sheet having excellent oxidation resistance and high-temperature strength, and method for producing same |
| US9938598B2 (en) | 2011-02-17 | 2018-04-10 | Nippon Steel & Sumikin Stainless Steel Corporation | High-purity ferritic stainless steel sheet with excellent oxidation resistance and high-temperature strength, and process for producing the same |
| GB2549729A (en) * | 2016-04-26 | 2017-11-01 | Skf Magnetic Mechatronics | Method of manufacturing a lamination stack for use in an electrical machine |
| CN114410944A (en) * | 2021-12-24 | 2022-04-29 | 苏州钢特威钢管有限公司 | Manufacturing process method for preventing super ferrite stainless steel pipe from cold rolling cracking |
Also Published As
| Publication number | Publication date |
|---|---|
| JP2763141B2 (en) | 1998-06-11 |
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