JPH0417615A - Production of stainless steel sheet having excellent corrosion resistance and working moldability - Google Patents
Production of stainless steel sheet having excellent corrosion resistance and working moldabilityInfo
- Publication number
- JPH0417615A JPH0417615A JP12065290A JP12065290A JPH0417615A JP H0417615 A JPH0417615 A JP H0417615A JP 12065290 A JP12065290 A JP 12065290A JP 12065290 A JP12065290 A JP 12065290A JP H0417615 A JPH0417615 A JP H0417615A
- Authority
- JP
- Japan
- Prior art keywords
- less
- stainless steel
- corrosion resistance
- steel sheet
- pickling
- 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
- 230000007797 corrosion Effects 0.000 title claims abstract description 74
- 238000005260 corrosion Methods 0.000 title claims abstract description 74
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 36
- 239000010935 stainless steel Substances 0.000 title claims abstract description 34
- 238000004519 manufacturing process Methods 0.000 title claims description 15
- 238000000137 annealing Methods 0.000 claims abstract description 24
- 238000005554 pickling Methods 0.000 claims abstract description 21
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 13
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 10
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 230000001590 oxidative effect Effects 0.000 claims abstract description 6
- 229910052802 copper Inorganic materials 0.000 claims description 7
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- 229910052721 tungsten Inorganic materials 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- 229910052742 iron Inorganic materials 0.000 claims 3
- 239000007789 gas Substances 0.000 abstract description 12
- 238000005097 cold rolling Methods 0.000 abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 7
- 229910052717 sulfur Inorganic materials 0.000 abstract description 3
- 229910052758 niobium Inorganic materials 0.000 abstract description 2
- 229910052698 phosphorus Inorganic materials 0.000 abstract description 2
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 229910000831 Steel Inorganic materials 0.000 description 27
- 239000010959 steel Substances 0.000 description 27
- 238000012360 testing method Methods 0.000 description 23
- 230000000694 effects Effects 0.000 description 19
- 239000000203 mixture Substances 0.000 description 7
- 229920006395 saturated elastomer Polymers 0.000 description 6
- 238000011156 evaluation Methods 0.000 description 5
- 230000006866 deterioration Effects 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910052760 oxygen Inorganic materials 0.000 description 4
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 3
- 229910052684 Cerium Inorganic materials 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 3
- 239000001301 oxygen Substances 0.000 description 3
- 150000003839 salts Chemical class 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- 229910000680 Aluminized steel Inorganic materials 0.000 description 2
- 230000002378 acidificating effect Effects 0.000 description 2
- 239000004480 active ingredient Substances 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000005868 electrolysis reaction Methods 0.000 description 2
- WABPQHHGFIMREM-UHFFFAOYSA-N lead(0) Chemical compound [Pb] WABPQHHGFIMREM-UHFFFAOYSA-N 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- BDAGIHXWWSANSR-UHFFFAOYSA-N methanoic acid Natural products OC=O BDAGIHXWWSANSR-UHFFFAOYSA-N 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000010802 sludge Substances 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- OSWFIVFLDKOXQC-UHFFFAOYSA-N 4-(3-methoxyphenyl)aniline Chemical compound COC1=CC=CC(C=2C=CC(N)=CC=2)=C1 OSWFIVFLDKOXQC-UHFFFAOYSA-N 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- NHNBFGGVMKEFGY-UHFFFAOYSA-N Nitrate Chemical compound [O-][N+]([O-])=O NHNBFGGVMKEFGY-UHFFFAOYSA-N 0.000 description 1
- QAOWNCQODCNURD-UHFFFAOYSA-L Sulfate Chemical compound [O-]S([O-])(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-L 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 238000009825 accumulation Methods 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910021529 ammonia Inorganic materials 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 230000003750 conditioning effect Effects 0.000 description 1
- 238000004320 controlled atmosphere Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 125000004122 cyclic group Chemical group 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 230000002542 deteriorative effect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000003891 environmental analysis Methods 0.000 description 1
- 230000007613 environmental effect Effects 0.000 description 1
- 238000003912 environmental pollution Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 235000019253 formic acid Nutrition 0.000 description 1
- 239000011521 glass Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 239000000314 lubricant Substances 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 239000012528 membrane Substances 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000007935 neutral effect Effects 0.000 description 1
- 239000005416 organic matter Substances 0.000 description 1
- 238000011056 performance test Methods 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 229920000515 polycarbonate Polymers 0.000 description 1
- 239000004417 polycarbonate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 230000000284 resting effect Effects 0.000 description 1
- 230000002441 reversible effect Effects 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 239000007921 spray Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
Landscapes
- Heat Treatment Of Steel (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、自動車やオートバイエンジンなどの排気ガス
用マフラーやその前後の排気管系（以下総称してマフラ
ーという）なとに使用され、前記排気ガス系で生成する
湿潤カスや排気系カス凝縮液中で優れた耐食性と、マフ
ラー用素材に適用する際の複雑な成形にも優れた加工性
を示すステンレス鋼板の製造法に関するものである。Detailed Description of the Invention (Industrial Application Field) The present invention is used for exhaust gas mufflers of automobiles, motorcycle engines, etc., and exhaust pipe systems before and after the mufflers (hereinafter collectively referred to as mufflers). The present invention relates to a method for manufacturing a stainless steel sheet that exhibits excellent corrosion resistance in wet sludge generated in exhaust gas systems and exhaust system sludge condensate, and excellent workability for complex forming when applied to muffler materials.
（従来の技術）
ステンレス鋼板は、耐食性、耐高温酸化性、高温強度な
どの特性か活用される用途で飛躍的に需要が拡大しつつ
あり、その代表例として自動車、オートバイのマフラー
が挙げられる。エンジンで発生した高温の排気ガスは、
エギゾーストマニホールド、コンバーターなどを通過後
センターバイブ、マフラー、テールパイプを経て排気系
から排出される。エンジン始動時はマフラーの温度が低
いため排ガス中に水分が凝縮した凝縮液かマフラー内壁
面に付着し、またマフラー底部に滞留する。このように
生成した凝縮液中には、燃焼排気ガス中にあるＣｏ、’
−、ＮＨ４、Ｓ０４２Ｎｏ、−、その他ＣΩ−や微量の
有機物か含まれ、マフラーの耐食性に影響する。その過
程は、排気ガス温度の上昇とともにマフラーの温度も上
昇し、生成した凝縮液中に含まれるアンモニアなどが揮
発するため、凝縮液の液性はアルカリ性から酸性に変化
していく。(Prior Art) Demand for stainless steel sheets is rapidly increasing for applications where they are utilized for their properties such as corrosion resistance, high temperature oxidation resistance, and high temperature strength, and typical examples include mufflers for automobiles and motorcycles. The high temperature exhaust gas generated by the engine is
After passing through the exhaust manifold and converter, it is discharged from the exhaust system via the center vibe, muffler, and tail pipe. When the engine starts, the temperature of the muffler is low, so water condenses in the exhaust gas and condensate adheres to the inner wall of the muffler, and also accumulates at the bottom of the muffler. The condensate produced in this way contains Co,', which is present in the combustion exhaust gas.
-, NH4, S042No, -, and other CΩ- and trace amounts of organic matter, which affect the corrosion resistance of the muffler. In this process, as the exhaust gas temperature rises, the muffler temperature also rises, and ammonia and other substances contained in the generated condensate evaporate, causing the liquid property of the condensate to change from alkaline to acidic.
このような環境に適合したマフラーを作るには、従来は
、アルカリ性から酸性までの環境に対して耐食性を示す
アルミナイズド鋼板が主に採用されてきた。しかし、ア
ルミナイズド鋼板では到底期待寿命を達成することがで
きないことが明らかになるに従い、５〜１３％程度のＣ
「を添加した鋼板の適用、さらに最近では２０％近くの
Ｃｒを含んだステンレス鋼板の採用もなされている。In order to manufacture mufflers suitable for such environments, aluminized steel sheets, which exhibit corrosion resistance in environments ranging from alkaline to acidic, have been mainly used in the past. However, as it became clear that it was impossible to achieve the expected lifespan with aluminized steel sheets,
Cr-added steel sheets have been used, and more recently, stainless steel sheets containing nearly 20% Cr have also been adopted.
−船釣にステンレス鋼板は、熱延、熱延酸洗かなされた
のち、ゼンジマーミルで代表される小径ロール（直径的
１００ｍｍ）でリバース冷延される。- Stainless steel sheets for boat fishing are hot-rolled, hot-rolled and pickled, and then reverse cold-rolled using small-diameter rolls (100 mm in diameter), such as a Sendzimer mill.
ついで軟化焼鈍される。焼鈍によるテンパーカラー発生
を避ける際には光輝焼鈍炉が適用される。Then, it is softened and annealed. A bright annealing furnace is used to avoid the occurrence of temper color due to annealing.
また、表面にテンパーカラーが発生し、そのままの状態
では外観、溶接作業性、プレス成型性などの而で実用上
問題かある場合は、酸洗、塩浴処理、中性塩電解処理な
どで表面仕上げが施されている。In addition, if temper color occurs on the surface and there is a practical problem with appearance, welding workability, press formability, etc. in that state, the surface should be treated with pickling, salt bath treatment, neutral salt electrolysis treatment, etc. Finished.
しかし、近年の排気ガス規制強化に伴い、マフラーは使
用条件が厳しくなるとともに、製作条件も形状、構造面
で複雑多様になってきた。このような動向に対しで、前
記したような鋼板で製造されたマフラーは十分な耐食性
とパフォーマンス性を得ることかできないため、自動車
の安全性、長寿命化、経済性を達成する、より優れた耐
食性材料が望まれていた。こうした要求に対しで、すて
に５％から１０％Ｃｒ含有鋼（特開昭６３−１４３２４
０号公報、６３−１４３２４１号公報参照）が提案され
たり、従来から市販されている既製のフェライト系ステ
ンレス鋼板が使用されていることは前述した通りである
。However, with the tightening of exhaust gas regulations in recent years, the usage conditions for mufflers have become stricter, and the manufacturing conditions have also become more complex and diverse in terms of shape and structure. In response to these trends, mufflers manufactured from steel plates as mentioned above cannot have sufficient corrosion resistance and performance, so we are developing better mufflers that achieve automobile safety, longer life, and economic efficiency. Corrosion-resistant materials were desired. In response to these demands, steel containing 5% to 10% Cr (Japanese Patent Application Laid-Open No. 63-14324
As mentioned above, ferritic stainless steel sheets have been proposed (see Japanese Patent No. 0 and No. 63-143241), and commercially available ready-made ferritic stainless steel sheets have been used.
（発明が解決しようとする課題）
本発明は、こうした状況を踏まえてあらためて実際に使
用されているマフラーの実態を詳細に（腐食形態・環境
分析など）解析し、その結果に基づいて得られた腐食環
境条件下でステンレス鋼の主要成分であるＣｒ 、Ｍｏ
、Ｎｉの成分の影響、さらにＣｕ 、Ｎｂ 、Ｗ、Ｖ
、Ｚｒのそれぞれ単独、あるいは共存添加時の耐食性（
局部腐食の発生・停止特性；以下耐食性という）におよ
ほす影響を検討し、各元素の効果を明確にすることによ
り、実際のマフラーへの適用においても優れた耐食性を
示し、当該機器の長寿命化・安全性・環境汚染防止など
を長期にわたって確保することを可能にすると共にプレ
ス成形性を大幅に向上した自動車・オートバイなどのエ
ンジン排ガス用ステンレス鋼の製造法を提供することを
目的とするものである。(Problems to be Solved by the Invention) In light of these circumstances, the present invention has analyzed in detail (corrosion form, environmental analysis, etc.) the actual conditions of mufflers actually used, and has been developed based on the results. Cr, Mo, the main components of stainless steel under corrosive environmental conditions
, the influence of Ni components, as well as Cu, Nb, W, and V
, Zr when added alone or in combination (
By examining the effects of each element on the onset and stop characteristics of localized corrosion (hereinafter referred to as corrosion resistance) and clarifying the effects of each element, we have demonstrated excellent corrosion resistance even when applied to actual mufflers, and have shown that the long-term use of the equipment The purpose is to provide a method for producing stainless steel for engine exhaust gas from automobiles, motorcycles, etc., which makes it possible to ensure longevity, safety, and prevention of environmental pollution over a long period of time, as well as greatly improving press formability. It is something.
（課題を解決するための手段）
上記目的を達成するために本発明の要旨とするところは
、重量％で
Ｃ・０．００５％以上０．０５％以下、Ｓｉ：０．０１
％以上０．８％以下、
Ｍｎ：０．０５％以上１．５％以下、
Ｃｒ：１２％以上１８．５％以下、
Ｍｏ：０．２％以上３．０％以下、
１） ： ０．００５％以上０．１％以下、Ｎ、０、旧
％以下を含有して
Ｔｉ ：０．０５％以上１．０％以下およびＮｂ：０
．０５％以上１．０％以下の１種又は２種を含存し、
あるいはさらに、
Ｎｉ：０．１％以上１．０％以下、
Ｃｕ：０．０３％以上１．０％以下、
Ｗ ＋０．０５％以上０５％以下、
Ｖ ：０．０５％以上０．５％以下およびＺｒ：０．
０５％以上１ 、０％以下のＩＦｉまたは２種を含有し
、
あるいはさらにまた、
Ｃａ ： ０．００１％以上０．０３％以下およびＣｅ
： ０．００１％以上０．０３％以下の１種または２
種を含有して残部Ｆｅおよび不可避的不純物からなるス
テンレス鋼を、大径ロールで冷間圧延し、さらに露点±
０℃〜−４０℃の弱酸化性雰囲気中で、８２５〜９７５
℃の温度範囲で軟化焼鈍し、しかる後に酸洗仕上げをほ
どこすステンレス鋼板の製造法である。(Means for Solving the Problems) In order to achieve the above object, the gist of the present invention is that C: 0.005% or more and 0.05% or less, Si: 0.01% by weight.
% or more and 0.8% or less, Mn: 0.05% or more and 1.5% or less, Cr: 12% or more and 18.5% or less, Mo: 0.2% or more and 3.0% or less, 1): 0. Contains 0.05% or more and 0.1% or less, N, 0, old% or less, Ti: 0.05% or more and 1.0% or less, and Nb: 0
．． Ni: 0.1% or more and 1.0% or less, Cu: 0.03% or more and 1.0% or less, W +0 .05% or more and 0.5% or less, V: 0.05% or more and 0.5% or less, and Zr: 0.
Contains 0.05% or more 1, 0% or less of IFi or 2, or furthermore, Ca: 0.001% or more and 0.03% or less and Ce.
: Type 1 or 2 of 0.001% or more and 0.03% or less
Stainless steel containing seeds and the remainder Fe and unavoidable impurities is cold rolled with large diameter rolls and further reduced to a dew point of ±
825-975 in a weakly oxidizing atmosphere at 0°C to -40°C
This is a manufacturing method for stainless steel sheets that is softened and annealed at a temperature range of 10°C and then subjected to pickling finishing.
二のように、本発明は該鋼板の成分と冷延作業以降の製
造条件とを組み合わせることによってその特性を大幅に
向上させうろことができた。すなわち、冷延において大
径ロールを採用することにより、プレス成型時に重要な
特性であるランクフォード値が飛躍的に向上すること、
その後の制御雰囲気中での軟化焼鈍と酸洗処理との組み
合わせで耐食性が向上すること、また、その処理によっ
てプレス時の製品表面潤滑性が向上しで、すぐれたプレ
ス成型を付与するものである。Second, in the present invention, the properties of the steel sheet can be greatly improved by combining the composition of the steel sheet and the manufacturing conditions after cold rolling. In other words, by using large diameter rolls in cold rolling, the Lankford value, which is an important characteristic during press forming, can be dramatically improved.
The subsequent combination of softening annealing in a controlled atmosphere and pickling treatment improves corrosion resistance, and this treatment also improves the surface lubricity of the product during pressing, giving it excellent press forming properties. .
以下、本発明について詳細に説明する。The present invention will be explained in detail below.
（作 用） 以下、上記した鋼板の成分限定理由について述べる。(for production) The reason for limiting the composition of the steel sheet described above will be described below.
ＣＴＣは、ステンレス鋼の耐食性に有害であるが、強度
の観点からは、ある程度の含有量が必要である。０．０
０５％未満の極低炭素量では製造コストが高くなる。ま
た、０．０５％を越えると耐食性は大幅に劣化するため
０．００５％以上０．０５％以下とした。Although CTC is harmful to the corrosion resistance of stainless steel, a certain amount of CTC is necessary from the viewpoint of strength. 0.0
An extremely low carbon content of less than 0.5% increases manufacturing costs. Moreover, if it exceeds 0.05%, the corrosion resistance will be significantly deteriorated, so the content is set to 0.005% or more and 0.05% or less.
Ｓｉ；Ｓｉは０．０．０１％以上添加されると後述する
軟化焼鈍処理時に表面に生成する酸化膜中に他の元素よ
り優先的に蓄積し耐食性に有効な元素、たとえばＣｒ、
Ｍｏか鋼中から表面へ拡散消費される結果惹起される耐
食性劣化を抑制する効果をもたらす。このＳｉの効果は
温度、時間、雰囲気との組み合わせにおいて０，５％を
越えるとその効果は飽和に達し、０．８％を越えると加
工性が問題となる。Si: When Si is added in an amount of 0.0.01% or more, it accumulates preferentially over other elements in the oxide film formed on the surface during the softening annealing treatment described later, and is an element effective for corrosion resistance, such as Cr,
This has the effect of suppressing corrosion resistance deterioration caused by Mo diffused and consumed from the inside of the steel to the surface. The effect of Si reaches saturation when it exceeds 0.5% in combination with temperature, time, and atmosphere, and when it exceeds 0.8%, processability becomes a problem.
Ｃｒ；Ｃｒは、本発明の基本成分である。凝縮液を含む
環境など高い耐食性を要求される環境ではＭ□さらに必
要に応じてＮｉ、Ｃｕなどと共存の形で１２％以上の添
加が必要である。多いほど耐食性、耐酸化性は向上する
が、１８．５％を越えてもその耐食性は飽和する。又、
作り込みか難しく経済的にも高価となる。Cr; Cr is a basic component of the present invention. In an environment where high corrosion resistance is required, such as an environment containing condensate, it is necessary to add 12% or more of M□ and, if necessary, coexist with Ni, Cu, etc. Corrosion resistance and oxidation resistance improve as the amount increases, but even if it exceeds 18.5%, the corrosion resistance is saturated. or,
It is difficult to manufacture and economically expensive.
Ｍｎ；Ｍｎは、排ガス凝縮液環境での耐食性に特別に影
響を及はさないが、通常の成分含有量としで、０．０５
％以上１．５％以下を規定した。Mn; Mn does not particularly affect corrosion resistance in an exhaust gas condensate environment, but the normal component content is 0.05
% or more and 1.5% or less.
Ｍｏ；Ｍｏは、Ｃｒさらに必要に応じで、Ｎｊ。Mo; Mo is Cr and optionally Nj.
Ｃｕなどと共存の形で添加され、加工性を向上し、また
凝縮液環境での局部腐食発生、進展を抑制するために必
須の元素である。０．２％以上３．０％以下の添加でＣ
ｒ、およびその他の特許請求の範囲記載の各成分（以下
その他元素という）との共存で極めて効果的となる。０
．２％未満では、耐食性は、不十分となるが、３，０％
を越えても耐食性の改善にそれほど寄与しないし、且つ
、高価となる。It is added in coexistence with Cu, etc., and is an essential element for improving workability and suppressing the occurrence and progression of local corrosion in a condensate environment. C with addition of 0.2% or more and 3.0% or less
It becomes extremely effective in coexistence with r and each of the other components (hereinafter referred to as other elements) described in the claims. 0
．． If it is less than 2%, the corrosion resistance will be insufficient, but if it is less than 3.0%, the corrosion resistance will be insufficient.
Even if it exceeds this value, it does not contribute much to improving corrosion resistance and becomes expensive.
Ａｐ、Ａｌｌは、鋼の結晶粒を微細化して成形後の表面
外観劣化を防止する成分で、０．１％以下の範囲で添加
されるが０．１％を越えると耐食性、熱間加工性を劣化
させる。また、０．００５％未満では効果がない。Ap and All are components that refine the crystal grains of steel and prevent deterioration of the surface appearance after forming. They are added in a range of 0.1% or less, but if they exceed 0.1%, corrosion resistance and hot workability are reduced. deteriorate. Further, if it is less than 0.005%, there is no effect.
Ｎ、Ｎは、ＰおよびＳ成分と同様に不可避的成分で、ス
テンレス鋼の耐食性を劣化させるので、少ない程良い。N and N, like the P and S components, are unavoidable components and degrade the corrosion resistance of stainless steel, so the smaller the better.
０．０１％以下とした。The content was set to 0.01% or less.
Ｐ；Ｐは、凝縮液環境における耐食性に影響するので、
少ない程良い。０．０２５％を越えると耐食性が劣化す
る。P; P affects corrosion resistance in a condensate environment, so
The less the better. If it exceeds 0.025%, corrosion resistance will deteriorate.
ＳＯ５も、凝縮液環境における耐食性に影響する元素で
低い程よい。上限を０．０１０％とした。SO5 is also an element that affects corrosion resistance in a condensate environment, and the lower the better. The upper limit was set to 0.010%.
Ｎｂ；Ｎｂは、ＣまたはＮを固定し、ステンレス鋼の耐
食性の劣化を防ぐ。耐食性を向上するため０．０５％か
ら１．０％の範囲で添加される。１．０％を越えると熱
間加工性を劣化させる。０．０５％未満ては効果がない
。Nb; Nb fixes C or N and prevents deterioration of the corrosion resistance of stainless steel. It is added in a range of 0.05% to 1.0% to improve corrosion resistance. If it exceeds 1.0%, hot workability deteriorates. Less than 0.05% has no effect.
Ｔｉ：ＴＩは、ＣまたはＮを固定し、ステンレス鋼の耐
食性の劣化を防ぐ。Ｃａと共存してＯを固定し、Ｓｉ、
Ｍｎの酸化物の生成を抑制し、熱間加工性と耐食性を向
上させる。００５％以上１．０％以下添加される。１．
０％を越えると熱間加工性を劣化させる。Ti: Ti fixes C or N and prevents deterioration of the corrosion resistance of stainless steel. Coexists with Ca to fix O, Si,
Suppresses the formation of Mn oxides and improves hot workability and corrosion resistance. 0.005% or more and 1.0% or less. 1.
If it exceeds 0%, hot workability deteriorates.
本発明においで、上記のような鋼成分組成で製造された
鋼板は耐食性と加工成形性がすぐれている。さらに本発
明はこれらの特性を一層改善するためにＮｉ、Ｃｕなど
の鋼成分を含有させる。In the present invention, the steel plate manufactured with the steel composition as described above has excellent corrosion resistance and workability. Furthermore, in the present invention, steel components such as Ni and Cu are contained in order to further improve these properties.
Ｎｉ；Ｎｊは、本発明ステンレス鋼の選択添加成分であ
る。凝縮液を含む環境など高い耐食性を要求される環境
では、Ｃｒ、Ｍｏ、その他元素と共存して用いられる。Ni; Nj is a selectively added component of the stainless steel of the present invention. In environments where high corrosion resistance is required, such as environments containing condensate, it is used in coexistence with Cr, Mo, and other elements.
局部腐食進展抑制に効果的であるが、０．１％未満では
効果がなく、１．０％を越えるとその効果は飽和し、ま
た、経済的にも高価となる。It is effective in suppressing the progress of local corrosion, but if it is less than 0.1% it is ineffective, and if it exceeds 1.0% the effect is saturated and it becomes economically expensive.
Ｃｕ；Ｃｕは、Ｃｒ、Ｍｏをベースとした成分系、さら
にＮｌｓその他元素と共存の形で添加され、凝縮液を含
む環境での耐食性を得るための添加元素である。０．０
３％以上で共存効果が著しく、また１、０％を越えると
耐食性は飽和し、且つ熱間加工性を劣化させる。Cu: Cu is an additive element that is added in a component system based on Cr and Mo, and coexisting with Nls and other elements to obtain corrosion resistance in an environment containing condensate. 0.0
At 3% or more, the coexistence effect is significant, and at more than 1.0%, corrosion resistance is saturated and hot workability is deteriorated.
Ｗ；Ｗの共存添加は、ステンレス鋼の耐食性、局部腐食
性を向上させるので、必要に応じて０．５％以下で添加
する。０．５％を越えるとその効果は飽和する。０．０
５％未満では効果はない。W: Since the co-addition of W improves the corrosion resistance and local corrosion resistance of stainless steel, it is added in an amount of 0.5% or less as necessary. If it exceeds 0.5%, the effect is saturated. 0.0
There is no effect if it is less than 5%.
ｖ；Ｖの共存添加は、ステンレス鋼の耐食性、局部腐食
性を向上させるので、必要に応じて０．５％以下で添加
する。０，５％を越えるとその効果は飽和する。０．０
５％未満では効果はない。v; Since the co-addition of V improves the corrosion resistance and local corrosion resistance of stainless steel, it is added in an amount of 0.5% or less as necessary. If it exceeds 0.5%, the effect is saturated. 0.0
There is no effect if it is less than 5%.
Ｚｒ；Ｚｒの共存添加は、ステンレス鋼の耐食性、局部
腐食性を向上させるので、必要に応じて１．０％以下で
添加する。 １．０％を越えるとその効果は飽和する。Zr: Since the co-addition of Zr improves the corrosion resistance and local corrosion resistance of stainless steel, it is added in an amount of 1.0% or less as necessary. If it exceeds 1.0%, the effect is saturated.
０．０５９（ｉ未満では効果はない。There is no effect below 0.059 (i).
Ｃａ、Ｃｅ ；Ｃａ、Ｃｅは、低硫黄鋼中でＡｇと共存
してＯを固定し、凝縮液中での局部腐食の発生起点とな
り得るＭｎＳ系の介在物の生成を抑制し、耐食性を改善
する。Ｃａ、Ｃｅは、それぞれ０．００１〜０．０３％
の範囲で１種または２種が必要に応じて添加される。Ca, Ce; Ca, Ce coexists with Ag in low sulfur steel and fixes O, suppresses the formation of MnS-based inclusions that can be the starting point of local corrosion in condensate, and improves corrosion resistance. do. Ca and Ce are each 0.001 to 0.03%
One or two types may be added as necessary within the following range.
上記のような鋼成分組成の鋼板は、通常の鋼板製造工程
を経で、ステンレス熱延鋼板あるいはさらに焼鈍などの
熱処理を施した後、大径ロール（直径１１０ｍｍ以上）
で冷間圧延し、焼鈍する。大径ロールの冷間圧延は、加
工性すなわちランクフォード値を向上させる。第１図は
１５％Ｃｒ−０，１９％Ｔｌ−０，０７％Ａｊ７−０．
００７％Ｃ成分系で、焼鈍温度を８２５℃に統一した場
合の、ロール直径とランクフォード（ｒ）値の関係に対
するＭａｉｌの効果を示す。すなわちランクフォード値
は、Ｍｏ成分を含有する鋼板を大径ロールで冷間圧延し
、焼鈍することによって向上する。Steel sheets with the above steel compositions are processed through the normal steel sheet manufacturing process into stainless steel hot-rolled steel sheets or after further heat treatment such as annealing, into large-diameter rolls (diameter 110 mm or more).
Cold rolled and annealed. Cold rolling with large diameter rolls improves workability, ie Lankford value. Figure 1 shows 15%Cr-0, 19%Tl-0, 07%Aj7-0.
This figure shows the effect of Mail on the relationship between roll diameter and Lankford (r) value when the annealing temperature is unified to 825° C. in a 007% C component system. That is, the Lankford value is improved by cold rolling a steel plate containing the Mo component with large diameter rolls and annealing it.
この場合の焼鈍作業は冷延されて硬化したステンレス鋼
板を軟質化させるのが第１目的であるか、本発明におい
ては高温にさらされる結果生成する酸化膜の特性をコン
トロールすることで、焼鈍に引き続いて行われる酸洗作
業で好適な表面状態を確保することも、この焼鈍作業の
大きな目的である。In this case, the primary purpose of annealing is to soften the cold-rolled and hardened stainless steel sheet, or in the present invention, the annealing process is performed by controlling the characteristics of the oxide film that is formed as a result of exposure to high temperatures. Another major purpose of this annealing operation is to ensure a suitable surface condition for the subsequent pickling operation.
酸化膜の厚みを左右する重要な因子は、焼鈍板温である
。この板温は、焼鈍炉に導入される鋼板の成分、特にＳ
ｉの量、および炉内の湿度（露点）の関係で決まる反応
で生ずる酸化膜の厚みによって制御される。本発明の成
分系は、再結晶開始温度は７７５℃から％０℃であり、
組織、軟質度を安定させるためにはそれぞれの温度より
も高い温度でしかも表面の酸化膜は後述する酸洗による
鋼板の表面調整に適した厚みが生成される温度で焼鈍す
る必要がある。種々の実験の結果、本発明の成分系では
９７５℃を越えると後述する露点±０℃では酸化膜か厚
くなりすぎ、露点が一４０℃より低いと酸化膜が緻密に
なりすぎるため、酸洗後の外観を劣化させたり、生産性
を低下させる問題かある。An important factor that influences the thickness of the oxide film is the annealing plate temperature. This plate temperature is determined by the composition of the steel plate introduced into the annealing furnace, especially S
It is controlled by the thickness of the oxide film produced by the reaction, which is determined by the relationship between the amount of i and the humidity (dew point) in the furnace. In the component system of the present invention, the recrystallization start temperature is from 775°C to %0°C,
In order to stabilize the structure and softness, it is necessary to anneal at a temperature higher than the respective temperatures, and at a temperature at which the oxide film on the surface is formed to a thickness suitable for surface conditioning of the steel plate by pickling, which will be described later. As a result of various experiments, it was found that in the composition system of the present invention, if the temperature exceeds 975°C, the oxide film becomes too thick at the dew point of ±0°C, which will be described later, and if the dew point is lower than 140°C, the oxide film becomes too dense. There are problems with deteriorating the subsequent appearance and reducing productivity.
また、板温か８２５℃より低いと酸化膜中へのＳｉの蓄
積か不十分であるから本願の目的か達成されない。した
かっで、焼鈍温度は８２５℃から９７５℃に限定した。Further, if the plate temperature is lower than 825° C., the purpose of the present invention cannot be achieved because the accumulation of Si in the oxide film is insufficient. Therefore, the annealing temperature was limited to 825°C to 975°C.
酸化膜の厚みは焼鈍雰囲気の中に含まれる気体成分、と
くに酸素の量によっても大きく左右される。酸化膜厚み
か大き過ぎると、のちに行われる酸洗によって表面が過
度に荒らされて外観上商品価値を下げる。また、酸化膜
厚みが薄すぎるとそれが原因となって後述するような有
効成分濃度低下層の排除、表面非金属介在物の除去が果
たせなくなる。種々の試験結果から、本発明成分のステ
ンレス鋼板成分、焼鈍板温度で適正な酸化膜厚みを確保
するためには、焼鈍炉内の酸素濃度を露点で検出して±
０℃〜−４０℃が適当である。たとえば、板温か８５０
℃で、１６％Ｃｒ−１，２％Ｍ。The thickness of the oxide film is also greatly influenced by the amount of gas components, especially oxygen, contained in the annealing atmosphere. If the oxide film is too thick, the surface will be excessively roughened by pickling, which will reduce the commercial value in terms of appearance. Furthermore, if the oxide film is too thin, it becomes impossible to eliminate the active ingredient concentration lowering layer and remove surface non-metallic inclusions as described later. From various test results, in order to ensure an appropriate oxide film thickness at the stainless steel plate composition of the present invention and the annealing plate temperature, the oxygen concentration in the annealing furnace must be detected by the dew point and ±
A temperature of 0°C to -40°C is suitable. For example, board temperature 850
16%Cr-1,2%M at °C.
００１５％ＴＩを主成分とする鋼板を各種の温度で焼鈍
した場合の酸化膜の生成状態をグロー放電分光分析計（
以下ＧＤＳと略記）で調査した結果を第２図に示す。す
なわち（ａ）図における露点か一２０℃で操業された酸
化膜の厚さＴに比べで、露点＋ｌＯ℃では酸化膜が厚す
ぎ、−５０℃では薄すぎる。A glow discharge spectrometer (
Figure 2 shows the results of the survey using GDS (hereinafter abbreviated as GDS). That is, compared to the thickness T of the oxide film operated at a dew point of -20°C in Figure (a), the oxide film is too thick at a dew point of +10°C and too thin at -50°C.
このようにして焼鈍されたステンレス鋼板は、続いて酸
洗する。ステンレス鋼板の酸洗は、たとえば特公昭８Ｂ
−４５４８０号公報のように厚い酸化膜が存在すると商
品価値を下げるほかに、絞り加工する時にダイスの寿命
が短縮する弊害を除くことである。しかし、本発明者ら
の検討によると、本発明の成分系において適正な酸洗を
施すことにより、鋼板の耐食性を大幅に向上する。The stainless steel plate thus annealed is then pickled. For pickling stainless steel plates, for example, the Tokuko Showa 8B
The purpose is to eliminate the disadvantage that the existence of a thick oxide film as in Japanese Patent No. 45480 not only reduces the commercial value but also shortens the life of the die during drawing. However, according to studies conducted by the present inventors, the corrosion resistance of steel sheets can be significantly improved by performing appropriate pickling in the component system of the present invention.
さらに説明をすると、本成分系の成分を焼鈍すると表面
に酸化膜が生成する。この場合、酸化膜中には酸素との
親和力がＦｅより強い元素が優先的に蓄櫃し、その部分
の直下ではこれら成分の濃度低下現象をきたす。この現
象は、Ｓｉの作用で抑制されるが、耐食性向上の目的で
添加されたＣｒ、Ｍｏ、Ｎｉ 、Ｃｕなどに対しては有
害である。この有効成分欠乏現象は酸洗作業で救済され
る。とりわけ、鋼板がＮｏ３−、Ｃｒｂ−イオンを含む
酸洗液中で陰・極電解される場合に素地の溶解で顕著で
あるから、酸洗作業中、鋼板か陰極電解状態で１回以上
行われる交番電解酸洗作業でその効果は大きい。To explain further, when the components of this component system are annealed, an oxide film is formed on the surface. In this case, elements that have a stronger affinity for oxygen than Fe accumulate preferentially in the oxide film, and the concentration of these components decreases immediately below that portion. Although this phenomenon is suppressed by the action of Si, it is harmful to Cr, Mo, Ni, Cu, etc. added for the purpose of improving corrosion resistance. This active ingredient deficiency phenomenon can be alleviated by pickling. Particularly, when a steel plate is subjected to cathodic electrolysis in a pickling solution containing No3- and Crb- ions, the dissolution of the substrate is noticeable, so during pickling work, the steel plate is cathodic electrolyzed more than once. The effect is great in alternating electrolytic pickling work.
また、ステンレス鋼の場合、表面に存在する非金属介在
物は発銹点、隙間腐食促進作用をもたらすので極力排除
すべきである。本発明における酸洗による表面清浄化は
、表面に存在するこの非金属介在物の除去にも効果的で
あり、その結果耐食性が更に向上する。Furthermore, in the case of stainless steel, non-metallic inclusions present on the surface should be avoided as much as possible since they cause rusting points and promote crevice corrosion. Surface cleaning by pickling in the present invention is also effective in removing nonmetallic inclusions present on the surface, and as a result, corrosion resistance is further improved.
更に、素地の酸洗により表面は微細な凹凸を呈する。こ
れはプレス成型時の潤滑液保持作用に寄与するので、実
用上有効である。Furthermore, the surface exhibits minute irregularities due to pickling of the substrate. This is practically effective because it contributes to the lubricant retention effect during press molding.
（実 施 例） 本発明品の緒特性を実施例により説明する。(Example) The characteristics of the product of the present invention will be explained using examples.
第１表に示した本発明鋼および比較鋼は、それぞれ−膜
内に行われる方法で溶製、加熱、熱延、酸洗されたのち
、直径が４００ｍｍの冷延ロールで冷間圧延されたのち
、表中に記載した条件で軟化焼鈍、酸洗されたのち性能
試験に供した。The inventive steel and the comparative steel shown in Table 1 were melted, heated, hot-rolled, and pickled using the in-membrane method, respectively, and then cold-rolled using cold-rolling rolls with a diameter of 400 mm. Afterwards, it was subjected to a softening annealing and pickling under the conditions listed in the table, and then subjected to a performance test.
第１表の局部腐食発生電位は、前述の電気化学的な局部
腐食発生評価試験によって得られた値で、この値が大き
いほど局部腐食か発生し難いことを示す。The local corrosion occurrence potential in Table 1 is a value obtained by the electrochemical local corrosion occurrence evaluation test described above, and the larger this value is, the more difficult it is to cause local corrosion.
局部腐食評価試験は、第３図に示した局部腐食評価試験
用試験片を用いた。第３図中、１はリード線、２は試験
面以外をシールした部分、３は試験面、４はポリカーボ
ネート製ボルト・ナツトを示す。これにより試験面上に
人工的に隙間を生成し、局部腐食の発生を加速できるよ
うにした。この試験片を用いで、模擬凝縮液環境中で第
４図に示すように自然電位（Ｅ、。１．）より、電位を
アノード方向に２０ｍＶ／ｗｉｎで掃引したとき、電流
密度が１００μＡ／ｃ−を越えた点の電位を局部腐食発
生電位と規定した。この電位が大きい値を示すほど、局
部腐食は発生し難い傾向を示す。For the local corrosion evaluation test, the test piece for local corrosion evaluation test shown in FIG. 3 was used. In FIG. 3, 1 is a lead wire, 2 is a sealed portion other than the test surface, 3 is a test surface, and 4 is a polycarbonate bolt/nut. This created an artificial gap on the test surface, making it possible to accelerate the occurrence of localized corrosion. Using this test piece, when the potential was swept in the anode direction at 20 mV/win from the natural potential (E, 1.) as shown in Figure 4 in a simulated condensate environment, the current density was 100 μA/c. The potential at a point exceeding - was defined as the local corrosion potential. The larger this potential value is, the less likely local corrosion is to occur.
また、局部腐食深さの最大値は、凝縮液環境においで、
幅（Ｗ）：５０關、長さ（Ｎ）：８０關、板厚（ｔ）：
１．２龍の形状の試験片を用い、試験片表面を＃３２０
研磨後、脱脂しで、浸漬試験を行った。In addition, the maximum local corrosion depth in a condensate environment is
Width (W): 50mm, Length (N): 80mm, Thickness (t):
1.2 Using a dragon-shaped test piece, the surface of the test piece is #320.
After polishing, it was degreased and an immersion test was conducted.
なお、試験環境は、硫酸イオン（５０００ｐｐｎ＋）
、炭酸イオン（３０００ｐｐｍ） 、塩化物イオン（３
０００ｐｐＩ１１）、硝酸イオン（１０（ｌｐｐｍ）
、ギ酸（１００ｐｐＩＩｌ）を所定の量添加調整して作
製した凝縮液を用いた。試験方法は、硝子製ビーカー（
２００ｃｃ）を用い、この中に試験片を立てておき、試
験片の半分まで浸漬されるように凝縮ｄｌｏｏｃｃを入
れた。その後、ビーカーを沸騰条件で２時間加熱し、２
４時間静止を３０日間繰り返した。試験後試験片上に観
察された局部腐食の深さをすべて測定し、その内の最大
深さで評価した。The test environment was sulfate ion (5000ppn+)
, carbonate ion (3000ppm), chloride ion (3
000ppI11), nitrate ion (10(lppm)
A condensate prepared by adjusting the addition of a predetermined amount of formic acid (100 ppII) was used. The test method is to use a glass beaker (
200cc) was used, the test piece was stood up in this, and the condensed dloocc was poured so that it was immersed up to half of the test piece. After that, heat the beaker under boiling conditions for 2 hours,
Resting for 4 hours was repeated for 30 days. After the test, all the depths of local corrosion observed on the test piece were measured, and the maximum depth was evaluated.
また、実用状況を想定した腐食試験法としてマフラー内
部腐食模擬試験、改良塩水噴霧試験（ＭＳＴ）、サイク
リック腐食試験（ＣＣＴ）を採用した。In addition, a muffler internal corrosion simulation test, modified salt spray test (MST), and cyclic corrosion test (CCT) were adopted as corrosion test methods assuming practical situations.
（発明の効果）
本発明鋼は、第１表の局部腐食発生特性、および局部腐
食深さから比較鋼に比べ、いずれの鋼種もすぐれた耐食
性を示していた。このことから本発明鋼は、エンジン排
ガス環境のような腐食性の厳しい凝縮液環境においで、
長期にわたってすぐれた耐食性を示し、実用的に極めて
有効であることを示している。(Effects of the Invention) All of the steels of the present invention exhibited superior corrosion resistance compared to the comparative steels based on the local corrosion occurrence characteristics and local corrosion depth shown in Table 1. From this, the steel of the present invention can be used in a highly corrosive condensate environment such as an engine exhaust gas environment.
It shows excellent corrosion resistance over a long period of time, indicating that it is extremely effective in practical use.
第１図（ａ）は露点−２０℃で焼鈍した場合の酸化膜状
態をＧＤＳで調査したチャート、同じ＜（ｂ）は露点が
＋１０℃の場合、同じ＜（ｃ）は露点が一５０℃の場合
の状態を同一条件で調査したものである。
第２図は、冷延ロール径とランクフォード値の関係に対
するＭｏ添加量の効果を示したものである。
第３図（ａ）は、電気化学的な局部腐食発生評価試験に
用いた試験片形状を示す側面図、同（ｂ）は、その正面
図である。
第４図は、電気化学的な局部腐食発生評価試験法を説明
するための線図である。
１・・・リード線 ２・・・シール部３・・・
試験面 ４・・・ボルト・ナツト復代理人Figure 1 (a) is a GDS chart of the state of the oxide film when annealing is performed at a dew point of -20°C. Same < (b) shows the case when the dew point is +10°C, and same < (c) shows the dew point at -150°C. This is an investigation of the situation under the same conditions. FIG. 2 shows the effect of the amount of Mo added on the relationship between the cold rolling roll diameter and the Lankford value. FIG. 3(a) is a side view showing the shape of a test piece used in the electrochemical local corrosion occurrence evaluation test, and FIG. 3(b) is a front view thereof. FIG. 4 is a diagram for explaining an electrochemical local corrosion evaluation test method. 1...Lead wire 2...Seal part 3...
Test part 4... Boruto/Natsuto sub-agent
Claims (4)
なくとも１種を含有し、残部Ｆｅおよび不可避的不純物
からなるステンレス鋼を、大径ロールで冷間圧延し、さ
らに露点±０℃〜−４０℃の弱酸化性雰囲気中で、８２
５〜９７５℃の温度範囲で軟化焼鈍し、しかる後に酸洗
仕上げをほどこすことを特徴とする耐食性、加工成形性
のすぐれたステンレス鋼板の製造法。(1) In weight%, C: 0.005% or more and 0.05% or less, Si: 0.01% or more and 0.8% or less, Mn: 0.05% or more and 1.5% or less, Cr: 12% 18.5% or more, Mo: 0.2% or more and 3.0% or less, Al: 0.005% or more and 0.1% or less, N: 0.01% or less, and Ti: 0.05% or more. A stainless steel containing at least one selected from the group of 1.0% or less and Nb: 0.05% or more and 1.0% or less, and the balance consisting of Fe and unavoidable impurities is cold rolled with a large diameter roll. Furthermore, in a weakly oxidizing atmosphere with a dew point of ±0°C to -40°C,
A method for producing a stainless steel sheet with excellent corrosion resistance and processability, characterized by softening and annealing at a temperature range of 5 to 975°C, followed by pickling finish.
なくとも１種と、 Ｎｉ：０．１％以上１．０％以下、 Ｃｕ：０．０３％以上１．０％以下、 Ｗ：０．０５％以上０．５％以下、 Ｖ：０．０５％以上０．５％以下および Ｚｒ：０．０５％以上１．０％以下の群より選ばれた少
なくとも１種を含有し、残部Ｆｅおよび不可避的不純物
からなるステンレス鋼を、大径ロールで冷間圧延し、さ
らに露点±０℃〜−４０℃の弱酸化性雰囲気中で、８２
５〜９７５℃の温度範囲で軟化焼鈍し、しかる後に酸洗
仕上げをほどこすことを特徴とする耐食性、加工成形性
のすぐれたステンレス鋼板の製造法。(2) In weight%, C: 0.005% or more and 0.05% or less, Si: 0.01% or more and 0.8% or less, Mn: 0.05% or more and 1.5% or less, Cr: 12% 18.5% or more, Mo: 0.2% or more and 3.0% or less, Al: 0.005% or more and 0.1% or less, N: 0.01% or less, and Ti: 0.05% or more. At least one species selected from the group of 1.0% or less and Nb: 0.05% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cu: 0.03% or more1 .0% or less, W: 0.05% or more and 0.5% or less, V: 0.05% or more and 0.5% or less, and Zr: 0.05% or more and 1.0% or less. 1 type, with the remainder being Fe and unavoidable impurities, is cold rolled with large diameter rolls, and further heated to 82°C in a weakly oxidizing atmosphere with a dew point of ±0°C to -40°C.
A method for producing a stainless steel sheet with excellent corrosion resistance and processability, characterized by softening and annealing at a temperature range of 5 to 975°C, followed by pickling finish.
なくとも１種と、 Ｃａ：０．００１％以上０．０３％以下およびＣｅ：０
．００１％以上０．０３％以下の群より選ばれた少なく
とも１種を含有し、残部Ｆｅおよび不可避的不純物から
なるステンレス鋼を、大径ロールで冷間圧延し、さらに
露点±０℃〜−４０℃の弱酸化性雰囲気中で、８２５〜
９７５℃の温度範囲で軟化焼鈍し、しかる後に酸洗仕上
げをほどこすことを特徴とする耐食性、加工成形性のす
ぐれたステンレス鋼板の製造法。(3) In weight%, C: 0.005% or more and 0.05% or less, Si: 0.01% or more and 0.8% or less, Mn: 0.05% or more and 1.5% or less, Cr: 12% 18.5% or more, Mo: 0.2% or more and 3.0% or less, Al: 0.005% or more and 0.1% or less, N: 0.01% or less, and Ti: 0.05% or more. 1.0% or less and at least one species selected from the group of Nb: 0.05% or more and 1.0% or less, Ca: 0.001% or more and 0.03% or less, and Ce: 0
．． Stainless steel containing at least one element selected from the group of 0.001% or more and 0.03% or less, the balance consisting of Fe and unavoidable impurities, is cold rolled with a large diameter roll, and further has a dew point of ±0°C to -40°C. 825~ in a weakly oxidizing atmosphere at ℃
A method for producing a stainless steel sheet with excellent corrosion resistance and processability, which comprises softening and annealing in a temperature range of 975°C, followed by pickling finish.
なくとも１種と、 Ｎｉ：０．１％以上１．０％以下、 Ｃｕ：０．０３％以上１．０％以下、 Ｗ：０．０５％以上０．５％以下、 Ｖ：０．０５％以上０．５％以下および Ｚｒ：０．０５％以上１．０％以下の群より選ばれた少
なくとも１種と、 Ｃａ：０．００１％以上０．０３％以下およびＣｅ：０
．０１％以上０．０３％以下の群より選ばれた少なくと
も１種を含有し、残部Ｆｅおよび不可避的不純物からな
るステンレス鋼を、大径ロールで冷間圧延し、さらに露
点±０℃〜−４０℃の弱酸化性雰囲気中で、８２５〜９
７５℃の温度範囲で軟化焼鈍し、しかる後に酸洗仕上げ
をほどこすことを特徴とする耐食性、加工成形性のすぐ
れたステンレス鋼板の製造法。(4) In weight%, C: 0.005% or more and 0.05% or less, Si: 0.01% or more and 0.8% or less, Mn: 0.05% or more and 1.5% or less, Cr: 12% 18.5% or more, Mo: 0.2% or more and 3.0% or less, Al: 0.005% or more and 0.1% or less, N: 0.01% or less, and Ti: 0.05% or more. At least one species selected from the group of 1.0% or less and Nb: 0.05% or more and 1.0% or less, Ni: 0.1% or more and 1.0% or less, Cu: 0.03% or more1 .0% or less, W: 0.05% or more and 0.5% or less, V: 0.05% or more and 0.5% or less, and Zr: 0.05% or more and 1.0% or less. 1 type, Ca: 0.001% or more and 0.03% or less, and Ce: 0
．． Stainless steel containing at least one element selected from the group of 0.01% or more and 0.03% or less, the balance consisting of Fe and unavoidable impurities, is cold rolled with a large diameter roll, and further has a dew point of ±0°C to -40°C. 825-9 in a weakly oxidizing atmosphere at ℃
A method for producing a stainless steel sheet with excellent corrosion resistance and processability, which comprises softening and annealing in a temperature range of 75°C, followed by pickling finish.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2120652A JPH0774384B2 (en) | 1990-05-10 | 1990-05-10 | Manufacturing method of stainless steel sheet with excellent corrosion resistance and workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2120652A JPH0774384B2 (en) | 1990-05-10 | 1990-05-10 | Manufacturing method of stainless steel sheet with excellent corrosion resistance and workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0417615A true JPH0417615A (en) | 1992-01-22 |
| JPH0774384B2 JPH0774384B2 (en) | 1995-08-09 |
Family
ID=14791535
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2120652A Expired - Lifetime JPH0774384B2 (en) | 1990-05-10 | 1990-05-10 | Manufacturing method of stainless steel sheet with excellent corrosion resistance and workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0774384B2 (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002212683A (en) * | 2001-01-17 | 2002-07-31 | Kawasaki Steel Corp | Ferritic stainless steel sheet having excellent high temperature oxidation resistance |
| KR20030051050A (en) * | 2001-12-20 | 2003-06-25 | 현대자동차주식회사 | Stainless alloy with ferrite for automobile muffler |
| CN102337463A (en) * | 2011-09-28 | 2012-02-01 | 常熟市长江不锈钢材料有限公司 | 00Cr18Mo2 stainless steel pipe billet and manufacture method thereof |
| JP2016183400A (en) * | 2015-03-26 | 2016-10-20 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet excellent in corrosion resistance of burring processing part end surface and manufacturing method therefor |
| CN110629004A (en) * | 2019-10-29 | 2019-12-31 | 深圳万佳互动科技有限公司 | Heat treatment process of low-carbon stainless steel plate |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5782421A (en) * | 1980-11-10 | 1982-05-22 | Kawasaki Steel Corp | Bright annealing method of mo-containing middle cr concentration ferritic stainless steel |
| JPS5938334A (en) * | 1982-08-26 | 1984-03-02 | Nippon Steel Corp | Manufacture of ferritic stainless steel sheet with superior workability |
| JPS5983725A (en) * | 1982-11-06 | 1984-05-15 | Nippon Steel Corp | Preparation of ferrite type stainless steel thin plate free from surface flaw and low in ridging |
| JPS6393843A (en) * | 1986-10-07 | 1988-04-25 | Daido Steel Co Ltd | Stainless steel for cold forging |
-
1990
- 1990-05-10 JP JP2120652A patent/JPH0774384B2/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5782421A (en) * | 1980-11-10 | 1982-05-22 | Kawasaki Steel Corp | Bright annealing method of mo-containing middle cr concentration ferritic stainless steel |
| JPS5938334A (en) * | 1982-08-26 | 1984-03-02 | Nippon Steel Corp | Manufacture of ferritic stainless steel sheet with superior workability |
| JPS5983725A (en) * | 1982-11-06 | 1984-05-15 | Nippon Steel Corp | Preparation of ferrite type stainless steel thin plate free from surface flaw and low in ridging |
| JPS6393843A (en) * | 1986-10-07 | 1988-04-25 | Daido Steel Co Ltd | Stainless steel for cold forging |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002212683A (en) * | 2001-01-17 | 2002-07-31 | Kawasaki Steel Corp | Ferritic stainless steel sheet having excellent high temperature oxidation resistance |
| KR20030051050A (en) * | 2001-12-20 | 2003-06-25 | 현대자동차주식회사 | Stainless alloy with ferrite for automobile muffler |
| CN102337463A (en) * | 2011-09-28 | 2012-02-01 | 常熟市长江不锈钢材料有限公司 | 00Cr18Mo2 stainless steel pipe billet and manufacture method thereof |
| JP2016183400A (en) * | 2015-03-26 | 2016-10-20 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet excellent in corrosion resistance of burring processing part end surface and manufacturing method therefor |
| CN110629004A (en) * | 2019-10-29 | 2019-12-31 | 深圳万佳互动科技有限公司 | Heat treatment process of low-carbon stainless steel plate |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0774384B2 (en) | 1995-08-09 |
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