JP3314847B2 - Manufacturing method of ferritic stainless steel sheet with good workability - Google Patents
Manufacturing method of ferritic stainless steel sheet with good workabilityInfo
- Publication number
- JP3314847B2 JP3314847B2 JP13966795A JP13966795A JP3314847B2 JP 3314847 B2 JP3314847 B2 JP 3314847B2 JP 13966795 A JP13966795 A JP 13966795A JP 13966795 A JP13966795 A JP 13966795A JP 3314847 B2 JP3314847 B2 JP 3314847B2
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- steel sheet
- stainless steel
- temperature
- less
- ferritic stainless
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は高耐食性で、かつ深絞り
加工によって、成形品表面にリジングと呼ばれる微細凹
凸を生じなく、かつ二次加工性に優れたフェライト系ス
テンレス鋼板の製造法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing a ferritic stainless steel sheet which has high corrosion resistance, does not cause fine irregularities called ridging on the surface of a molded product by deep drawing, and has excellent secondary workability. It is.
【０００２】[0002]
【従来の技術】フェライト系ステンレス鋼板は厨房用機
器や家電機器などに広く使用され、流し台水槽で苛酷な
深絞り加工が施されている。また、自動車部品、家電部
品、建材部材などにも用途が拡大しつつある。これは、
フェライト系ステンレス鋼板の製造技術が高純度化、特
殊元素添加などの面で向上し、耐食性が大幅に改善され
た他、深絞り加工性がＳＵＳ３０４に代表されるオース
テナイト系ステンレス鋼板のそれに匹敵するほどまで向
上したためである。これが、腐食性の厳しいこれら用途
のうちで、深絞り加工され、かつ厳しい腐食環境にさら
される、缶体、容器構造、管状部材にフェライト系ステ
ンレス鋼板が使用されはじめた理由である。2. Description of the Related Art Ferritic stainless steel sheets are widely used for kitchen appliances and home appliances, and are subjected to severe deep drawing in a sink water tank. In addition, applications are expanding to automobile parts, home electric parts, building materials and the like. this is,
The production technology of ferritic stainless steel sheets has been improved in terms of higher purity and addition of special elements, and the corrosion resistance has been greatly improved. This is because it has improved. This is the reason why ferritic stainless steel sheets have begun to be used for can bodies, container structures, and tubular members, which are deep drawn and exposed to severe corrosive environments, among these severely corrosive applications.
【０００３】しかし、深絞り加工を受けた後、さらに二
次加工を受け、かつ表面外観の優れていることが必要な
用途において、一次加工割れ、二次加工割れ、加工表面
に微細凹凸が発生するリジング現象が起こらないこと
は、従来技術で製造されたフェライト系ステンレス鋼板
では達成し得ず、改良技術の提案が待たれていた。[0003] However, in applications in which deep drawing is performed, secondary processing is required, and the surface appearance must be excellent, primary processing cracks, secondary processing cracks, and fine irregularities appear on the processed surface. The fact that the ridging phenomenon does not occur cannot be achieved with a ferritic stainless steel sheet manufactured by a conventional technique, and a proposal for an improved technique has been awaited.
【０００４】これらの要求のうちリジング改善に関する
方策の提案はなされているが、この要求を全部満たすも
のではない。例えば、特開昭６２−１９９７２１号公
報、特開平４−３４１５２１号公報は、フェライト系ス
テンレス鋼板の製造において熱延開始温度を特定の範囲
に限定し、熱延初期段階において３０〜６０秒のディレ
イを行うことによってリジング及び二次加工性を改善す
る方法を提案しているが、本来高速大量生産であるべき
熱延ラインの生産性が減ずることを余儀なくされる。ま
た、特開平４−１６０１１７号公報では、ディレイ圧延
の温度、時間、圧下率を限定する、及びこれらの技術と
最終圧延パスの温度、圧下率を限定することが提案され
ているがこれも同様に生産性を減じる。[0004] Among these demands, measures for improving ridging have been proposed, but do not satisfy all of the demands. For example, JP-A-62-197721 and JP-A-4-341521 limit the hot-rolling start temperature to a specific range in the production of a ferritic stainless steel sheet, and have a delay of 30 to 60 seconds in the initial stage of hot-rolling. However, a method for improving ridging and secondary workability by performing the above method has been proposed, but the productivity of the hot rolling line, which should be high-speed mass production, must be reduced. Japanese Patent Application Laid-Open No. 4-160117 proposes to limit the temperature, time and rolling reduction of delay rolling, and to limit these techniques and the temperature and rolling reduction of the final rolling pass. Reduce productivity.
【０００５】[0005]
【発明が解決しようとする課題】本発明は高耐食を保持
し、深絞りが可能で、二次加工においても割れが発生せ
ず、かつ加工表面にリジングが発生しないフェライト系
ステンレス鋼を熱延ラインの生産性を減ずることなく製
造する方法を提案するものである。SUMMARY OF THE INVENTION The present invention is a hot-rolled ferritic stainless steel which maintains high corrosion resistance, can be deep drawn, does not crack even in secondary working, and does not generate ridging on the worked surface. It is intended to propose a method of manufacturing without reducing the productivity of the line.
【０００６】[0006]
【課題を解決するための手段】フェライト系ステンレス
鋼板の耐食性を改善するには、粒界Ｃｒ減少による粒
界腐食を防止する、腐食電位を高める、腐食の進展
を抑制するなどの方策が考えられる。発明者らは、上記
原則を踏まえステンレス鋼中に存在する種々の元素の効
果を幅広く検討した。その結果、粒界腐食防止に対して
Ｔｉ，Ｎｂの添加、Ｃ，Ｎの抑制が有効であり、腐食電
位向上にはＣｕ添加、腐食進展の抑制にはＭｏ添加が効
果的であることを知見した。In order to improve the corrosion resistance of a ferritic stainless steel sheet, there are conceivable measures for preventing intergranular corrosion due to a decrease in grain boundary Cr, increasing the corrosion potential, and suppressing the progress of corrosion. . The inventors have extensively studied the effects of various elements present in stainless steel based on the above principle. As a result, it was found that the addition of Ti and Nb and the suppression of C and N were effective for preventing intergranular corrosion, the addition of Cu was effective for improving the corrosion potential, and the addition of Mo was effective for suppressing the progress of corrosion. did.
【０００７】そして、深絞り性付与には、Ｔｉ若しくは
Ｎｂの添加が有効であること、また、二次加工性の確保
にはＢ添加が有効であること、さらに、リジング性の向
上には熱延終了後の熱処理条件を検討し、比較的低温で
長時間、中温で短時間、高温でごく短時間の熱処理を施
すことで本発明特定の成分系に対してリジングが発生し
ない条件を見出した。[0007] The addition of Ti or Nb is effective for imparting deep drawability, the addition of B is effective for ensuring secondary workability, and the addition of heat is effective for improving ridging properties. After examining the heat treatment conditions after the completion of the elongation, it was found that ridging does not occur for the specific component system of the present invention by applying a heat treatment for a relatively long time at a relatively low temperature, a short time at a medium temperature, and a very short time at a high temperature. .
【０００８】本発明は上記知見を基に構成したもので、
その要旨とするところは、Ｃ ：０．００１〜０．０３
０％、 Ｓｉ：１．０％以下、Ｍｎ：１．０％以下、
Ｃｒ：１５．０〜２２．０％、Ａｌ：０．
００２〜０．１５０％、 Ｍｏ：０．４〜２．０％、Ｔ
ｉ：０．０２〜０．７０％でかつＴｉ／（Ｃ＋Ｎ）≧
６、Ｃｕ：０．１０〜０．６０％、 Ｂ ：０．０
００３〜０．００５０％を含有し、残部が鉄及び不可避
的不純物からなるフェライト系ステンレス鋼板を、 通常の熱間圧延を行った後、８００〜９００℃の温度
で３〜１５時間加熱し、その後冷間圧延、軟化焼鈍を行
うこと、 熱間圧延を行った後、直ちに鋼板温度を７５０〜８５
０℃の温度に保定するカバー内に導入し、６０〜９０分
保持し、その後冷間圧延、軟化焼鈍を行うこと、 熱間圧延を行った後、直ちに鋼板を９５０〜１０５０
℃の温度で３０〜９０秒加熱し、その後冷間圧延、軟化
焼鈍を行うこと を特徴とする加工仕上がり性の良いフェライト系ステン
レス鋼板の製造法である。ここで、熱間圧延、冷間圧
延、軟化焼鈍は通常の方法で良い。また、軟化焼鈍の後
必要に応じて通常の表面仕上げを行っても良い。The present invention is based on the above findings,
The summary is that C: 0.001 to 0.03
0%, Si: 1.0% or less, Mn: 1.0% or less,
Cr: 15.0 to 22.0%, Al: 0.
002-0.150%, Mo: 0.4-2.0%, T
i: 0.02 to 0.70% and Ti / (C + N) ≧
6, Cu: 0.10 to 0.60%, B: 0.0
A ferritic stainless steel sheet containing 003 to 0.0050%, with the balance being iron and unavoidable impurities, is subjected to normal hot rolling, and then heated at a temperature of 800 to 900 ° C for 3 to 15 hours, and thereafter Cold rolling, soft annealing, hot rolling, immediately after the steel sheet temperature 750-85
After being introduced into a cover kept at a temperature of 0 ° C. and kept for 60 to 90 minutes, cold rolling and softening annealing are performed.
This is a method for producing a ferritic stainless steel sheet having good workability, characterized by heating at a temperature of 30 ° C. for 30 to 90 seconds, followed by cold rolling and soft annealing. Here, the hot rolling, the cold rolling, and the soft annealing may be performed by ordinary methods. After the soft annealing, a normal surface finishing may be performed as necessary.
【０００９】[0009]
【作用】以下本発明を詳細に説明する。 《Ａ》成分に関して 本発明における成分の数値限定の根拠を説明する。Ｃは
耐食性を確保する目的で必要量範囲で限定される。Ｃは
含有量が少ないほど良いが、０．００１％未満にするた
めには過大な設備と、多大な時間を要するので実用的で
ない。Ｃが存在することはＣｒとの結合による（Ｃｒ−
Ｃの生成）→（周辺Ｃｒ濃度低下）→（耐食性劣化）を
惹起する。後述するＴｉの添加はこのＣｒ−Ｃ形成を防
止する目的で添加されるものであるが、製造工程中の冷
却速度、成品実用中の加工・加熱などでＴｉ，Ｎｂの効
果が消失することがあるので、Ｃ量が０．０３０％を超
えると耐食性は期待どおりに発揮されないから、本発明
のＣ量は０．００１〜０．０３０％に限定される。The present invention will be described below in detail. << A >> Component The grounds for limiting the numerical value of the component in the present invention will be described. C is limited in a necessary amount range for the purpose of securing corrosion resistance. The lower the content of C, the better, but it is not practical to reduce the content to less than 0.001% because it requires excessive equipment and a large amount of time. The existence of C is due to the bond with Cr (Cr-
(Generation of C) → (decrease in peripheral Cr concentration) → (deterioration of corrosion resistance). The addition of Ti, which will be described later, is for the purpose of preventing the formation of Cr-C, but the effects of Ti and Nb may be lost due to the cooling rate during the manufacturing process, processing and heating during the practical use of the product. Therefore, if the C content exceeds 0.030%, the corrosion resistance is not exhibited as expected, so the C content of the present invention is limited to 0.001 to 0.030%.
【００１０】Ｓｉの量は制限される。Ｓｉは素材の強度
を高めたり、耐高温酸化性を向上させるので用途によっ
ては奨励されるが、本発明品が使われる耐食性、加工性
用途では制限され、その量は１．０％以下が良い。[0010] The amount of Si is limited. Si is recommended for some applications because it enhances the strength of the material and improves high-temperature oxidation resistance, but is limited in the corrosion resistance and workability applications where the present invention is used, and the amount is preferably 1.0% or less. .
【００１１】Ｍｎの量は制限される。Ｍｎは素材の強度
を高めたり、耐食性に悪影響を及ぼすＳの害を消去する
ため添加される。本発明の用途では強度が過度に高いと
実用しにくいのでＭｎ量は１．０％以下に制限される。[0011] The amount of Mn is limited. Mn is added in order to increase the strength of the material and to eliminate harmful effects of S that adversely affect corrosion resistance. In the application of the present invention, if the strength is excessively high, it is difficult to use the Mn content, so the Mn content is limited to 1.0% or less.
【００１２】Ｃｒは必要量添加される。Ｃｒは本発明品
に耐食性を付与する基本元素である。様々な耐食性を評
価した結果、Ｃｒが１５％未満であると発銹、腐食進展
が多く、不都合であった。また、Ｃｒが２２％を超える
と、実用的な耐食性は飽和し、硬質さ、製造しにくさ、
コストアップなどの不都合を生じた。したがってＣｒ濃
度は１５．０〜２２．０％が望ましい。[0012] Cr is added in a required amount. Cr is a basic element that imparts corrosion resistance to the product of the present invention. As a result of evaluating various corrosion resistances, if the Cr content was less than 15%, rusting and corrosion progressed much, which was inconvenient. On the other hand, if the Cr content exceeds 22%, the practical corrosion resistance is saturated, and the hardness, the difficulty in manufacturing,
Inconveniences such as cost increase occurred. Therefore, the Cr concentration is desirably 15.0 to 22.0%.
【００１３】Ａｌは必要量添加される。Ａｌは製鋼時の
脱酸材として利用されるが、その量が０．００２％未満
ではその効果がなく、また０．１５０％以上では硬質
さ、耐食性劣化などの不都合を生じる。したがって、Ａ
ｌは０．００２〜０．１５０％に制限される。Al is added in a required amount. Al is used as a deoxidizing material in steel making. However, if its amount is less than 0.002%, it has no effect, and if it is 0.150% or more, inconveniences such as hardness and corrosion resistance deterioration occur. Therefore, A
l is limited to 0.002-0.150%.
【００１４】Ｔｉは必要量添加される。Ｔｉは耐食性を
劣化させるＣ，Ｎを自らがＴｉ−Ｃ，Ｔｉ−Ｎとして固
定させるため、耐食性を確保するのに必須の元素であ
る。０．０２％未満、（Ｃ＋Ｎ）＜６ではＣ，Ｎを完全
に固定させ得ず、耐食性が確保できない。また、０．７
０％を超えるとその効果は飽和し、製造コスト上も好ま
しくない。したがって、Ｔｉは０．０２〜０．７０％で
かつＴｉ／（Ｃ＋Ｎ）≧６の量に限定される。[0014] Ti is added in a required amount. Ti is an element essential for securing corrosion resistance because it fixes C and N, which degrade corrosion resistance, as Ti-C and Ti-N by itself. If it is less than 0.02% and (C + N) <6, C and N cannot be completely fixed, and the corrosion resistance cannot be secured. Also, 0.7
If it exceeds 0%, the effect is saturated, which is not preferable in terms of manufacturing cost. Therefore, Ti is limited to an amount of 0.02 to 0.70% and Ti / (C + N) ≧ 6.
【００１５】Ｍｏは耐食性向上のため必要量添加され
る。Ｍｏはステンレス鋼特有の孔食の進展を抑制する。
０．４％未満ではその効果に乏しく、２．０％を超すと
効果が飽和し、コストがかさむ。したがって、Ｍｏは
０．４〜２．０％に制限される。Mo is added in a necessary amount to improve corrosion resistance. Mo suppresses the progress of pitting corrosion peculiar to stainless steel.
If it is less than 0.4%, the effect is poor, and if it exceeds 2.0%, the effect is saturated and the cost increases. Therefore, Mo is limited to 0.4 to 2.0%.
【００１６】Ｃｕは耐食性向上のため必要量添加され
る。Ｃｕは多くの腐食環境における全面腐食を抑制し、
特に酸性環境では飛躍的に耐食性を向上させる。０．１
０％未満ではその効果に乏しく、０．６０％を超すと効
果が飽和する。したがってＣｕは０．１０〜０．６０％
に限定される。Cu is added in a necessary amount for improving corrosion resistance. Cu suppresses general corrosion in many corrosive environments,
Particularly in an acidic environment, the corrosion resistance is dramatically improved. 0.1
If it is less than 0%, the effect is poor, and if it exceeds 0.60%, the effect is saturated. Therefore, Cu is 0.10 to 0.60%
Is limited to
【００１７】Ｂは二次加工性（深絞り加工後の張り出し
成形性）向上のため必要量添加される。０．０００３％
未満では効果が発揮されず、０．００５０％を超すと深
絞り性が劣化するとともに鋼片の割れが発生する。B is added in a necessary amount for improving the secondary workability (the stretch formability after deep drawing). 0.0003%
If it is less than 0.0050%, the effect will not be exhibited, and if it exceeds 0.0050%, the deep drawability will be deteriorated and the billet will crack.
【００１８】《Ｂ》熱延焼鈍に関して 通常の熱間圧延工程を経た後、通常の冷間圧延、軟化焼
鈍、必要に応じて行う表面仕上げの間で施される加熱・
焼鈍は、リジング性を改善する目的で行われる。この加
熱・焼鈍がリジング防止に役立つメカニズムは熱延組織
中で起こる再結晶である。再結晶した組織が冷延工程で
破壊されることでリジング発生の根源となる冷延・焼鈍
後のコロニー成長を抑制するのである。<< B >> Regarding hot rolling annealing After passing through a normal hot rolling step, heating / heating performed during normal cold rolling, softening annealing, and surface finishing performed as necessary.
Annealing is performed for the purpose of improving ridging properties. The mechanism by which this heating and annealing helps to prevent ridging is recrystallization that occurs in the hot rolled structure. When the recrystallized structure is destroyed in the cold rolling process, the growth of colonies after cold rolling and annealing, which is a source of ridging, is suppressed.
【００１９】加熱は、鋼板を８００〜９００℃の温度
で３〜１５時間加熱する方法、熱間圧延終了直後のコ
イル巻き取り状態で鋼板を７５０〜８５０℃の温度に保
定するカバー内に導入し、６０〜９０分保持する方法、
鋼板を９５０〜１０５０℃の温度で３０〜９０秒加熱
する方法がある。Heating is performed by heating the steel sheet at a temperature of 800 to 900 ° C. for 3 to 15 hours. The steel sheet is introduced into a cover for maintaining the temperature at a temperature of 750 to 850 ° C. in a coil wound state immediately after completion of hot rolling. Holding for 60-90 minutes,
There is a method of heating a steel sheet at a temperature of 950 to 1050 ° C. for 30 to 90 seconds.
【００２０】鋼板を８００〜９００℃の温度で３〜１５
時間加熱する方策は主として箱型焼鈍設備で施される。
温度が８００℃未満で効果を確保しようとすると保定時
間は極端に長くなり、経済的でない。また、９００℃を
超すと表面の酸化現象が進行し素地のＣｒ濃度が減少す
るいわゆる脱Ｃｒ現象が起こり、使用性能が劣化する。
加熱時間が３時間未満であると温度を９００℃にしても
効果が得られず、１５時間を超すと加熱温度が８００℃
でも前述の脱Ｃｒ現象が起こる。The steel sheet is heated at a temperature of 800 to 900 ° C. for 3 to 15
The method of heating for time is mainly performed in a box-type annealing facility.
If the effect is to be ensured at a temperature lower than 800 ° C., the retention time becomes extremely long, which is not economical. On the other hand, when the temperature exceeds 900 ° C., the so-called “de-Cr” phenomenon in which the oxidation phenomenon of the surface proceeds and the Cr concentration of the base material decreases, and the use performance deteriorates.
If the heating time is less than 3 hours, the effect cannot be obtained even if the temperature is 900 ° C., and if the heating time is more than 15 hours, the heating temperature is 800 ° C.
However, the aforementioned Cr removal phenomenon occurs.
【００２１】熱間圧延終了直後の巻き取り状態で鋼板を
７５０〜８５０の温度に６０〜９０分保持する方法は主
として熱延工場のライン内で採用される。この方法は温
度条件と時間条件とを組み合わせて実施される。７５０
℃未満の温度では加熱時間を９０分以上にしても効果が
ない。また、８５０℃を超える温度ではカバー内に導入
されることで結晶粒の粗大化が起こり実用性に問題が生
じる。この方法において、他の二種の方法より緩やかな
加熱条件で同様の効果が得られるメカニズムは次のごと
く推定される。すなわち、温度降下過程では鋼板マトリ
ックス中で各種析出反応、変態挙動などが非平衡的に進
んでいると思われるが、この過程で鋼板温度を抑制する
ことは、カーバイドの析出、粒成長などの点で他の二種
とは異なる効果があると思われる。The method of holding the steel sheet at a temperature of 750 to 850 for 60 to 90 minutes in a wound state immediately after the end of hot rolling is mainly employed in a hot rolling mill line. This method is performed by combining temperature conditions and time conditions. 750
At a temperature lower than ℃, even if the heating time is 90 minutes or more, there is no effect. At a temperature exceeding 850 ° C., the crystal grains are coarsened by being introduced into the cover, which causes a problem in practicality. In this method, the mechanism by which the same effect can be obtained under milder heating conditions than the other two methods is estimated as follows. In other words, it is thought that various precipitation reactions and transformation behaviors are progressing in a non-equilibrium manner in the steel sheet matrix during the temperature drop process, but controlling the steel sheet temperature in this process is important in terms of precipitation of carbide, grain growth, etc. It seems to have different effects from the other two.
【００２２】鋼板を連続焼鈍炉の中で９５０〜１０５０
℃の温度に３０〜９０秒加熱する方法をとると他の２法
より短時間でリジング性が向上する。この場合、温度が
９５０℃未満では９０秒以上の加熱を要し、ラインが長
大になる。また１０５０℃を超えると結晶粒の粗大化を
起こし実用性に問題がある。The steel sheet is placed in a continuous annealing furnace at 950 to 1050.
If the method of heating at a temperature of 30 ° C. for 30 to 90 seconds is used, the ridging property is improved in a shorter time than the other two methods. In this case, if the temperature is lower than 950 ° C., heating for 90 seconds or more is required, and the line becomes long. On the other hand, when the temperature exceeds 1050 ° C., the crystal grains become coarse, and there is a problem in practicality.
【００２３】[0023]
【実施例】表１に示すような本発明品と従来鋼の成分鋼
を転炉で溶製し通常の鋳造法によって鋼片とした後、熱
間圧延により板厚６mmの熱延コイルとした。ついで発明
品については表に示した熱延焼鈍を行い、さらに通常の
冷間圧延、焼鈍を行って板厚０．８mmの冷延鋼帯とし
た。EXAMPLE The steels of the present invention and the conventional steels as shown in Table 1 were melted in a converter and made into billets by a normal casting method, and then hot-rolled into hot-rolled coils having a thickness of 6 mm. . Next, the invention product was subjected to hot rolling annealing as shown in the table, and further to ordinary cold rolling and annealing to obtain a cold rolled steel strip having a sheet thickness of 0.8 mm.
【００２４】これを表１に併記した条件（記載条件以外
は通常の方法によった）で製造し、耐食性、深絞り性、
リジング性及び二次加工性を調査した結果を示した。本
発明によった鋼板は従来法によった鋼板より優れた諸性
能を示した。This was produced under the conditions described in Table 1 (except for the conditions described below, which were obtained by a usual method).
The results of examining the ridging property and the secondary workability are shown. The steel sheet according to the present invention showed various performances superior to the steel sheet according to the conventional method.
【００２５】[0025]
【表１】 [Table 1]
【００２６】[0026]
【表２】 [Table 2]
【００２７】[0027]
【発明の効果】以上のように本発明は近時需要が飛躍的
に増大しつつある高耐食性、高加工性（深絞り性、耐リ
ジング性、二次加工性）フェライト系ステンレス鋼板
を、効率的に製造することができる。また本発明品を使
用することにより、自動車排気系材料、家電製品などの
用途で従来より優れた製品が製造できることになるの
で、その経済的、社会的効能は極めて大きい。As described above, according to the present invention, high corrosion resistance, high workability (deep drawability, ridging resistance, secondary workability) ferritic stainless steel sheet, for which demand has been dramatically increasing in recent years, can be used efficiently. It can be manufactured in a special way. In addition, by using the product of the present invention, it is possible to produce a product superior to the conventional product for use in automobile exhaust system materials, home electric appliances, and the like, so that its economic and social effects are extremely large.
───────────────────────────────────────────────────── フロントページの続き (56)参考文献 特開 平５−112826（ＪＰ，Ａ) 特開 平５−78751（ＪＰ，Ａ) 特開 昭60−24326（ＪＰ，Ａ) 特開 昭58−199822（ＪＰ，Ａ) 特開 昭55−94445（ＪＰ，Ａ) (58)調査した分野(Int.Cl.7，ＤＢ名) C21D 9/46 - 9/48 C21D 8/00 - 8/04 C22C 38/00 - 38/60 ──────────────────────────────────────────────────続 き Continuation of the front page (56) References JP-A-5-112826 (JP, A) JP-A-5-78751 (JP, A) JP-A-60-24326 (JP, A) JP-A-58-58 199822 (JP, A) JP-A-55-94445 (JP, A) (58) Fields investigated (Int. Cl. 7 , DB name) C21D 9/46-9/48 C21D 8/00-8/04 C22C 38/00-38/60
Claims (3)
６、 Ｍｏ：０．４〜２．０％、 Ｃｕ：０．１０〜０．６０％、 Ｂ ：０．０００３〜０．００５０％を含有し、残部が
鉄及び不可避的不純物からなるフェライト系ステンレス
鋼板を、通常の熱間圧延を行った後、８００〜９００℃
の温度で３〜１５時間加熱し、その後冷間圧延、軟化焼
鈍を行うことを特徴とする加工仕上がり性の良いフェラ
イト系ステンレス鋼板の製造法。C: 0.001 to 0.030% by weight, Si: 1.0% or less, Mn: 1.0% or less, Cr: 15.0 to 22.0%, Al: 0. 002 to 0.150%, Ti: 0.02 to 0.70% and Ti / (C + N) ≧
6, Mo: 0.4 to 2.0%, Cu: 0.10 to 0.60%, B: 0.0003 to 0.0050%, the balance being ferrite stainless steel composed of iron and unavoidable impurities After the steel sheet is subjected to normal hot rolling, 800 to 900 ° C.
A method for producing a ferritic stainless steel sheet having good workability, characterized by heating at a temperature of 3 to 15 hours, followed by cold rolling and soft annealing.
６、 Ｍｏ：０．４〜２．０％、 Ｃｕ：０．１０〜０．６０％、 Ｂ ：０．０００３〜０．００５０％を含有し、残部が
鉄及び不可避的不純物からなるフェライト系ステンレス
鋼板を、熱間圧延を行った後、直ちに鋼板温度を７５０
〜８５０℃の温度に保定するカバー内に導入し、６０〜
９０分保持し、その後冷間圧延、軟化焼鈍を行うことを
特徴とする加工仕上がり性の良いフェライト系ステンレ
ス鋼板の製造法。2. C: 0.001 to 0.030% by weight, Si: 1.0% or less, Mn: 1.0% or less, Cr: 15.0 to 22.0%, Al: 0. 002 to 0.150%, Ti: 0.02 to 0.70% and Ti / (C + N) ≧
6, Mo: 0.4 to 2.0%, Cu: 0.10 to 0.60%, B: 0.0003 to 0.0050%, the balance being ferrite stainless steel composed of iron and unavoidable impurities Immediately after the steel sheet is hot-rolled, the steel sheet temperature is increased to 750.
Introduced into a cover maintained at a temperature of ~ 850 ° C,
A method for producing a ferritic stainless steel sheet having good workability, characterized by holding for 90 minutes and then performing cold rolling and soft annealing.
６、 Ｍｏ：０．４〜２．０％、 Ｃｕ：０．１０〜０．６０％、 Ｂ ：０．０００３〜０．００５０％を含有し、残部が
鉄及び不可避的不純物からなるフェライト系ステンレス
鋼板を、熱間圧延を行った後、直ちに鋼板を９５０〜１
０５０℃の温度で３０〜９０秒加熱し、その後冷間圧
延、軟化焼鈍を行うことを特徴とする加工仕上がり性の
良いフェライト系ステンレス鋼板の製造法。3. C: 0.001 to 0.030% by weight, Si: 1.0% or less, Mn: 1.0% or less, Cr: 15.0 to 22.0%, Al: 0. 002 to 0.150%, Ti: 0.02 to 0.70% and Ti / (C + N) ≧
6, Mo: 0.4 to 2.0%, Cu: 0.10 to 0.60%, B: 0.0003 to 0.0050%, the balance being ferrite stainless steel composed of iron and unavoidable impurities Immediately after hot rolling the steel sheet, the steel sheet
A method for producing a ferritic stainless steel sheet having good workability, characterized by heating at a temperature of 050 ° C. for 30 to 90 seconds, followed by cold rolling and soft annealing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13966795A JP3314847B2 (en) | 1995-06-06 | 1995-06-06 | Manufacturing method of ferritic stainless steel sheet with good workability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP13966795A JP3314847B2 (en) | 1995-06-06 | 1995-06-06 | Manufacturing method of ferritic stainless steel sheet with good workability |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08333639A JPH08333639A (en) | 1996-12-17 |
| JP3314847B2 true JP3314847B2 (en) | 2002-08-19 |
Family
ID=15250621
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP13966795A Expired - Lifetime JP3314847B2 (en) | 1995-06-06 | 1995-06-06 | Manufacturing method of ferritic stainless steel sheet with good workability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3314847B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR100415666B1 (en) * | 1999-12-20 | 2004-01-31 | 주식회사 포스코 | A ferritic stainless steel having improved formability, ridging resistance and a method for manufacturing it |
| JP5960951B2 (en) * | 2011-03-30 | 2016-08-02 | 新日鐵住金ステンレス株式会社 | Ferritic stainless steel sheet for automobile fuel tank with excellent fatigue characteristics and method for producing the same |
-
1995
- 1995-06-06 JP JP13966795A patent/JP3314847B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH08333639A (en) | 1996-12-17 |
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