JPH02170923A - Manufacture of cold rolled sheet of chromium stainless steel excellent in ridging resistance and press formability - Google Patents
Manufacture of cold rolled sheet of chromium stainless steel excellent in ridging resistance and press formabilityInfo
- Publication number
- JPH02170923A JPH02170923A JP32376288A JP32376288A JPH02170923A JP H02170923 A JPH02170923 A JP H02170923A JP 32376288 A JP32376288 A JP 32376288A JP 32376288 A JP32376288 A JP 32376288A JP H02170923 A JPH02170923 A JP H02170923A
- Authority
- JP
- Japan
- Prior art keywords
- stainless steel
- annealing
- cold rolling
- rolling
- ridging resistance
- 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.)
- Pending
Links
- 229910052804 chromium Inorganic materials 0.000 title claims abstract description 28
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 23
- 239000010935 stainless steel Substances 0.000 title claims abstract description 22
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 title claims description 28
- 239000011651 chromium Substances 0.000 title claims description 27
- 238000000137 annealing Methods 0.000 claims abstract description 56
- 238000005097 cold rolling Methods 0.000 claims abstract description 36
- 230000009466 transformation Effects 0.000 claims abstract description 10
- 238000005098 hot rolling Methods 0.000 claims description 11
- 238000000034 method Methods 0.000 abstract description 12
- 238000005554 pickling Methods 0.000 abstract description 2
- 229910045601 alloy Inorganic materials 0.000 abstract 1
- 239000000956 alloy Substances 0.000 abstract 1
- 239000002184 metal Substances 0.000 abstract 1
- 238000005096 rolling process Methods 0.000 description 18
- 229910000831 Steel Inorganic materials 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 239000010959 steel Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 238000009749 continuous casting Methods 0.000 description 3
- 238000010438 heat treatment Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 239000002253 acid Substances 0.000 description 1
- 238000004026 adhesive bonding Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 229910000734 martensite Inorganic materials 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 239000013589 supplement Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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）
この発明は、耐リジング性及びプレス加工性の極めて優
れたクロム系ステンレス鋼冷延板を、特に高い生産性の
下で効率良く製造し得る方法に関するものである。Detailed Description of the Invention (Field of Industrial Application) This invention enables efficient production of cold-rolled chromium-based stainless steel sheets with extremely excellent ridging resistance and press workability, particularly under high productivity. It is about the method.
（従来の技術）
クロム系ステンレス鋼板は、例えば連続鋳造又は造塊−
分塊圧延を経たスラブを、熱間圧延後クロム含有量に応
じてバッチ焼鈍又は連続焼鈍を行い、次いで必要に応じ
中間焼鈍をはさむ冷間圧延と、仕上げ焼鈍とを行って製
造される。(Prior art) Chromium-based stainless steel sheets are manufactured by, for example, continuous casting or ingot making.
After hot rolling, a slab subjected to blooming rolling is subjected to batch annealing or continuous annealing depending on the chromium content, and then cold rolling with intermediate annealing as necessary and final annealing are performed to produce the slab.
このような製造工程において、前記熱間圧延に続いて行
う焼鈍処理（熱延板焼鈍）は、耐リジング性及び成形性
の向上には不可欠な工程である。In such a manufacturing process, the annealing treatment (hot-rolled sheet annealing) performed subsequent to the hot rolling is an essential step for improving ridging resistance and formability.
クロム系ステンレス鋼で、ＳＵＳ ４１０やＳ［ＩＳ
４３０で代表される、クロム含有量が１７−ｔ％（以下
単に％で示す）以下の場合は、そのクロム含有■に応じ
ほぼ８００〜８５０℃以上の温度でＡｃ、変態が開始す
るため、この変態点温度以下に焼鈍温度が制限されるこ
とから熱延板焼鈍は、処理時間に数１０時間を要するハ
ツチ式焼鈍にて行う必要があり、生産性の著しい低下を
招く。Chrome-based stainless steel, SUS 410 and S [IS
When the chromium content is less than 17-t% (hereinafter simply expressed as %), as represented by 430, Ac transformation starts at a temperature of approximately 800 to 850°C or higher depending on the chromium content. Since the annealing temperature is limited to below the transformation point temperature, hot rolled sheet annealing must be performed by hatch type annealing which takes several tens of hours, resulting in a significant drop in productivity.
また１７％を超えるクロムを含有し、高温でもオーステ
ナイト相が析出しないフェライト単相ステンレス鋼や、
特公昭５７−２９５３２号公報のようにＳυ５４３０に
ＡＩ２等を添加することにより胱、変態点を高めた場合
では、約９００〜１０００″Ｃでの連続焼鈍により熱延
板焼鈍を行うことが可能であるが、熱間圧延中のオース
テナイト相の析出が無いかあるいは少ないために、熱延
集合Ｍｉ熾の発達が強く、耐リジング性が著しく劣る欠
点がある。In addition, ferritic single-phase stainless steel contains more than 17% chromium and does not precipitate austenite phase even at high temperatures.
In the case where the transformation point is increased by adding AI2 etc. to Sυ5430 as in Japanese Patent Publication No. 57-29532, it is possible to perform hot rolled sheet annealing by continuous annealing at about 900 to 1000"C. However, since there is no or little precipitation of the austenite phase during hot rolling, there is a drawback that the hot rolled agglomerated Mi grains are strongly developed and the ridging resistance is extremely poor.
また熱延板焼鈍の効果を補うために、必要な耐リジング
性及び成形性をを有するクロム系ステンレス鋼冷延板を
得るには、冷間圧延中に中間焼鈍と脱スケールを行うよ
うな極めて生産性の低い工程の介入が余儀な（される不
利があった。In addition, to supplement the effect of hot-rolled sheet annealing, in order to obtain cold-rolled chromium stainless steel sheets with the necessary ridging resistance and formability, intermediate annealing and descaling are performed during cold rolling. There was a disadvantage in that it forced intervention in processes with low productivity.
その他、熱間圧延時に低温度圧延又は強圧下圧延を行う
ことにより耐リジング性を向上させる方法もあるが、十
分な効果があるとは言えなかった。In addition, there is a method of improving ridging resistance by performing low temperature rolling or strong reduction rolling during hot rolling, but it could not be said that this was sufficiently effective.
（発明が解決しようとする課題）
従来−射的なりロム系ステンレス鋼冷延板の耐リジング
性及び成形性の向上手法として熱延板のバッチ焼鈍を行
った場合、生産性が阻害される問題があり、連続焼鈍で
は十分な耐リジング性が得られなかった問題についてを
利な解決を図り、良好な耐リジング性と成形性とを有す
るクロム系ステンレス鋼冷延板を、生産性を阻害するこ
となく効率良く製造し得る方法を提案することがこの発
明の目的である。(Problems to be Solved by the Invention) Conventional Problem: Productivity is hindered when batch annealing of hot rolled sheets is performed as a method for improving the ridging resistance and formability of cold-rolled steel sheets made of shot-rome stainless steel. We aim to solve the problem of not being able to obtain sufficient ridging resistance with continuous annealing, and create cold-rolled chromium-based stainless steel sheets with good ridging resistance and formability, which hinder productivity. It is an object of the present invention to propose a method that can be manufactured efficiently without any problems.
（課題を解決するための手段）
この発明では、上記の目的を達成するために軽度の予備
的な冷間圧延を、熱延板焼鈍に代わる軟化焼鈍前に施す
ことにより、該焼鈍時の再結晶を起こり易くし、その結
果軟化焼鈍後の冷間圧延を容易ならしめて著しく優れた
耐リジング性及びプレス加工性が得られることを見出し
た。この軟化焼鈍後の脱スケールは極めて容易であるこ
ともわかった。(Means for Solving the Problems) In order to achieve the above object, the present invention performs mild preliminary cold rolling before softening annealing instead of hot-rolled sheet annealing, thereby reproducing the annealing process. It has been found that crystallization is facilitated, and as a result, cold rolling after softening annealing is facilitated, resulting in extremely excellent ridging resistance and press workability. It was also found that descaling after this softening annealing is extremely easy.
すなわちこの発明は、クロムを１３．０〜２０．０％含
有するクロム系ステンレス鋼片を熱間圧延して熱延板を
得る段階、
この熱延板に圧下率２〜３０％の予備的な冷間圧延を施
す段階、
その後クロム含有量に応じＡｃ、変態点以下又は１１０
０℃以下でかつ７００℃以上の温度範囲で５分以内の軟
化焼鈍を行う段階、
次いで脱スケールと、製品板厚に減厚する冷間圧延及び
仕上げ焼鈍を施す段階
よりなること”を特徴とする耐リジング性及びプレス加
工性に優れたクロム系ステンレス鋼冷延板の製造方法で
ある。That is, the present invention includes a step of hot rolling a chromium-based stainless steel piece containing 13.0 to 20.0% chromium to obtain a hot rolled sheet, and a preliminary rolling reduction of 2 to 30% to the hot rolled sheet. Cold rolling step, then depending on the chromium content Ac, below the transformation point or 110
It is characterized by a step of performing softening annealing at a temperature of 0°C or lower and 700°C or higher for less than 5 minutes, followed by descaling, cold rolling to reduce the thickness of the product plate, and final annealing. This is a method for producing cold-rolled chromium-based stainless steel sheets with excellent ridging resistance and press workability.
ここでこの発明の基礎となった実験について説明する。Here, the experiment that formed the basis of this invention will be explained.
’） Ｏム系ステンレス鋼の典型例として表Ｉに示す成
分組成になる５ＩＩＳ ４１０及びＳＯ３４３０を公知
の方法（加熱温度１２００℃２圧下率９０％、圧延終了
温度８５０℃）で実験室ミルにて熱間圧延した厚さ４ｍ
ｍの熱延板を準備した。') 5IIS 410 and SO3430, which have the compositions shown in Table I as typical examples of O-based stainless steels, were prepared in a laboratory mill using a known method (heating temperature: 1200°C, reduction rate: 90%, rolling end temperature: 850°C). Hot rolled thickness 4m
A hot rolled sheet of m was prepared.
表１（−ｔ％）
これらの熱延板について圧下率５０％以下の１百囲で種
々の予備的な冷間圧延を施したのち、雲間（（中マＡｃ
、変態点温度直下で、ＳＵＳ ４１０に′つぃては８０
０℃で１分、ＳＯ３４３０ニ対しては８５０℃で１分の
軟化焼鈍を施した後、酸洗により脱スケールし、引き続
き１回法でｌ１ＭＩＩ＋厚に冷間圧延したのち、軟化焼
鈍と同じ条件で仕上げ焼鈍を行った。Table 1 (-t%) These hot-rolled sheets were subjected to various preliminary cold rolling at a rolling reduction of 50% or less, and then
, just below the transformation point temperature, SUS 410's temperature is 80
After performing softening annealing at 0°C for 1 minute and at 850°C for 1 minute for SO3430, descaling was performed by pickling, followed by cold rolling to l1MII+ thickness in one step, and then under the same conditions as softening annealing. Finish annealing was performed.
また比較として、熱延板に冷間圧延を施すことな（５Ｕ
Ｓ４１０については８００℃で１ ｈｒ、 ５ＵＳ４３
０ニツいては８５０℃でｌｈｒ熱延板焼鈍を行った後１
回法及び２回法で１１厚に冷間圧延を行った後ＳＵＳ／
１１０ニツイテは８００’Ｃ”ｉ？１分、５ｕＳ４３０
ニツイテは８５０℃で１分の仕上げ焼鈍を行った。In addition, for comparison, the hot-rolled sheet was not subjected to cold rolling (5U
1 hr at 800℃ for S410, 5US43
1 after lhr hot rolled sheet annealing at 850℃
After cold rolling to 11 thickness by two-step method and two-step method, SUS/
110 days is 800'C"i? 1 minute, 5uS430
Finish annealing was performed at 850°C for 1 minute.
かくして得られた鋼板について、リジングうねり高さ及
びプレス成形性の指標である下値を測定した結果を、予
備的な冷間圧延の圧下率と関連させて第１図に示す。The results of measuring the ridging waviness height and the lower value, which is an index of press formability, of the steel sheet thus obtained are shown in FIG. 1 in relation to the rolling reduction ratio of preliminary cold rolling.
同図から明らかなように、軟化焼鈍前の予備的な冷間圧
延は、耐リジング性の向上、ｒ値の向上に極めて効果が
あった。その効果は２％以上の圧下率で認められ、３０
％を超えると効果は飽和した。As is clear from the figure, preliminary cold rolling before softening annealing was extremely effective in improving ridging resistance and r value. The effect is recognized at a reduction rate of 2% or more, and 30
%, the effect was saturated.
また、３０％を超えると、熱間圧延時に生成したスケー
ルが鋼板に強く圧着し、かえって脱スケール性が劣化し
た。Moreover, when it exceeds 30%, the scale generated during hot rolling is strongly pressed against the steel plate, and the descaling performance is rather deteriorated.
この予備的な冷間圧延の圧下率は、１０％以上とするこ
とにより、従来のバッチ焼鈍後２回の冷延をおこなった
場合以上の耐リジング性とｒ値とが得られた。By setting the rolling reduction ratio of this preliminary cold rolling to 10% or more, it was possible to obtain ridging resistance and r value higher than that obtained when cold rolling was performed twice after conventional batch annealing.
これらの結果は、熱延板に対し予備的な冷間圧延により
歪導入を行った後、軟化焼鈍を施すことによって再結晶
が急速に生じたことによる。従来では、バッチ焼鈍後に
おいても圧延方向に伸長した再結晶組織が観察されるが
、この発明の方法によれば軟化焼鈍後に等軸化した再結
晶組織が得られた。These results are due to the rapid recrystallization caused by softening annealing after introducing strain into the hot rolled sheet through preliminary cold rolling. Conventionally, a recrystallized structure elongated in the rolling direction is observed even after batch annealing, but according to the method of the present invention, an equiaxed recrystallized structure was obtained after softening annealing.
以上のような予備的な冷間圧延の圧下率と、リジングう
ねり高さ及びｒ値との関係は、クロム系ステンレス鋼の
典型例である上記の実験鋼の他、クロムを１３，０〜２
０．０％含有するクロム系ステンレス鋼であれば変わり
はない。The relationship between the rolling reduction ratio of preliminary cold rolling, ridging waviness height, and r value as described above shows that in addition to the above experimental steel, which is a typical example of chromium-based stainless steel,
There is no difference if it is a chromium-based stainless steel containing 0.0%.
（作 用）
この発明で予備的な冷間圧延の圧下率、軟化焼鈍の温度
及び時間を限定した理由について説明する。(Function) The reason why the rolling reduction ratio of preliminary cold rolling and the temperature and time of softening annealing are limited in this invention will be explained.
予備的な冷間圧延の圧下率は、上述したように、２％に
満たないと耐リジング性の向上、ｒ値の向上に効果がな
い。好ましくは圧下率を１０％以上とすることにより、
従来のバッチ焼鈍後２回の冷延をおこなった場合以上の
耐リジング性とｒ値とが得られる。一方圧工率が３０％
を超えるとその効果は飽和し、熱間圧延時に生成したス
ケールが鋼板に強く圧着し、かえって脱スケール性が劣
化することがら圧下率は２〜３０％の範囲に限定した。As mentioned above, if the rolling reduction ratio in the preliminary cold rolling is less than 2%, it will not be effective in improving the ridging resistance and the r value. Preferably, by setting the rolling reduction ratio to 10% or more,
Ridging resistance and r value higher than those obtained by cold rolling twice after conventional batch annealing can be obtained. On the other hand, the compression ratio is 30%
If it exceeds this, the effect will be saturated and the scale generated during hot rolling will strongly press against the steel plate, which will actually deteriorate the descaling properties, so the rolling reduction was limited to a range of 2 to 30%.
軟化焼鈍温度は、７００℃に満たないと再結晶が生じに
くいので下限を７００℃とした。またこの焼鈍温度の上
限を、クロム含有量に応じて＾ｃ、変態点又は １１０
０℃以下とした理由は、Ａｃ１変態点を超える温度では
、焼鈍中に析出したオーステナイト相が、焼鈍後硬いマ
ルテンサイト和となってプレス加工性を劣化させるから
であり、クロム含有量が多く、高温でもフェライト単相
でオーステナイト相が析出しない場合では、焼鈍温度が
１１００℃を超えると結晶粒が粗大化し、製品を冷間加
工した際にオレンジピールを生じるからである。The lower limit of the softening annealing temperature was set at 700°C since recrystallization is difficult to occur if it is less than 700°C. Also, the upper limit of this annealing temperature is set to ^c, transformation point or 110 depending on the chromium content.
The reason for setting it below 0°C is that at temperatures exceeding the Ac1 transformation point, the austenite phase precipitated during annealing becomes a hard martensite sum after annealing and deteriorates press workability, and the chromium content is high. This is because if the annealing temperature exceeds 1100°C, the crystal grains will become coarse and orange peel will occur when the product is cold worked, in the case where the austenite phase does not precipitate with a single ferrite phase even at high temperatures.
軟化焼鈍の時間は、その温度に到達するだけで保持を行
う必要はないが、５分を超えると生産性が低下するので
５分以内とした。The softening annealing time was set to within 5 minutes, although it is not necessary to hold the temperature as long as it reaches that temperature, since productivity decreases if it exceeds 5 minutes.
次に、クロム含有量を限定した理由について説明する。Next, the reason for limiting the chromium content will be explained.
クロムは、クロム系ステンレス鋼の基本成分であり、充
分な耐食性を得るためには１３％以上含有させることが
必要なので下限を１３％とした。また含有量が２０％を
超えるとｒＡ板が硬質化しプレス成形性が劣化するので
上限を２０％とした。Chromium is a basic component of chromium-based stainless steel, and in order to obtain sufficient corrosion resistance it is necessary to contain it in an amount of 13% or more, so the lower limit was set at 13%. Moreover, if the content exceeds 20%, the rA plate becomes hard and press formability deteriorates, so the upper limit was set at 20%.
なおこの発明で熱間圧延条件、製品板厚に減厚する冷間
圧延条件及び仕上げ焼鈍条件については特に限定するも
のではなく、通常行われる条件を用いることができ、熱
間圧延条件については、加熱温度１０００〜１３００℃
１圧下率６０％以上、圧延終了温度７５０℃〜１０００
℃とするのが好ましく、製品板厚に滅厚する冷間圧延条
件については、圧下率４０％以上とするのが好ましく、
仕上げ焼鈍条件については、Ａ１変態温度あるいは１１
００℃以下で５分以下の保持とするのが好ましい。In this invention, the hot rolling conditions, the cold rolling conditions for reducing the thickness of the product plate, and the final annealing conditions are not particularly limited, and commonly used conditions can be used, and the hot rolling conditions are as follows: Heating temperature 1000-1300℃
1 rolling reduction rate 60% or more, rolling end temperature 750℃~1000℃
℃, and for cold rolling conditions that reduce the thickness of the product plate, it is preferable that the rolling reduction is 40% or more,
Regarding the final annealing conditions, A1 transformation temperature or 11
It is preferable to hold the temperature at 00°C or lower for 5 minutes or less.
（実施例）
表２に示す成分組成範囲になるＡ、Ｂ、Ｃ及びＤ鋼の４
種のクロム系ステンレス鋼連続鋳造スラブを準備し、こ
れらの連続鋳造スラブを１２００℃の温度で２００ ｍ
ｍ厚から４ｍｍ厚に熱間圧延し、表３に示す条件で予備
的な冷間圧延、軟化焼鈍後、混酸で脱スケールし、１回
法で１ｍｍｒｙ−に冷延後、軟化焼鈍と同じ温度で３０
秒間保持の仕上げ焼鈍を行った。(Example) 4 steels A, B, C and D having the composition range shown in Table 2
Prepare continuous casting slabs of chromium-based stainless steel, and test these continuous casting slabs for 200 m at a temperature of 1200°C.
After hot rolling from m thickness to 4 mm thickness, preliminary cold rolling and softening annealing under the conditions shown in Table 3, descaling with mixed acid, cold rolling to 1 mmry- in one step, and then at the same temperature as softening annealing. 30 at
Finish annealing was performed with a hold time of seconds.
かくして得られた鋼板のりジングうねり高さ（２０％引
張後表面粗度計で測定）及び下値（１５％引張後測定）
を測定した結果も表３に併記した。The thus obtained steel plate gluing waviness height (measured with a surface roughness meter after 20% tension) and lower value (measured after 15% tension)
The results of the measurements are also listed in Table 3.
同表から明らかなように、この発明に従う実施例は、適
切な予備的な冷間圧延条件及び軟化焼鈍条件を採用する
ことによって耐リジング性及びプレス加工性が極めて優
れていた。As is clear from the table, the examples according to the present invention had extremely excellent ridging resistance and press workability by adopting appropriate preliminary cold rolling conditions and softening annealing conditions.
これに対して予備的な冷間圧延を行わない従来例、予備
的な冷間圧延条件がこの発明の範囲から外れた比較例は
、耐リジング性ないしプレス加工性が劣っていた。On the other hand, conventional examples in which preliminary cold rolling was not performed and comparative examples in which preliminary cold rolling conditions were outside the scope of the present invention had poor ridging resistance and press workability.
（発明の効果）
この発明によれば、熱間圧延段階を経たクロム系ステン
レス熱延板に直接、予備的な冷間圧延を施した後で、従
来の熱延板焼鈍に代わる軟化焼鈍を付加することにより
、その後の脱スケールを経る製品板厚への冷間圧延工程
における生産性の阻害なしに耐リジング性及びプレス加
工性の極めて優れたクロム系ステンレス鋼冷延板を効率
良く製造することができる。(Effects of the Invention) According to the present invention, after directly performing preliminary cold rolling on a hot-rolled chromium-based stainless steel sheet, softening annealing is added in place of conventional hot-rolled sheet annealing. By doing so, it is possible to efficiently produce cold-rolled chromium-based stainless steel sheets with extremely excellent ridging resistance and press workability without hindering productivity in the subsequent cold-rolling process to produce product sheet thickness through descaling. Can be done.
第１図は、予備的な冷間圧延の圧下率と、その後の軟化
焼鈍を行った上で、脱スケール、製品板厚への冷間圧延
及び仕上焼鈍を行って得られる冷延板のりジングうねり
高さ及び下値との関係をしめずグラフである。Figure 1 shows the rolling reduction ratio of preliminary cold rolling, the subsequent softening annealing, descaling, cold rolling to product thickness, and final annealing to obtain a cold rolled plate. This is a graph showing the relationship between the undulation height and the lower value.
Claims (1)
系ステンレス鋼片を熱間圧延して熱延板を得る段階、 この熱延板に圧下率２〜３０％の予備的な冷間圧延を施
す段階、 その後クロム含有量に応じＡｃ＿１変態点以下又は１１
００℃以下でかつ７００℃以上の温度範囲で５分以内の
軟化焼鈍を行う段階、 次いで脱スケールと、製品板厚に減厚する冷間圧延及び
仕上げ焼鈍を施す段階 よりなることを特徴とする耐リジング性及びプレス加工
性に優れたクロム系ステンレス鋼冷延板の製造方法。[Claims] 1. A step of hot rolling a chromium-based stainless steel piece containing 13.0 to 20.0 wt% chromium to obtain a hot-rolled plate; A stage of preliminary cold rolling, then Ac_1 transformation point or below or 11 depending on the chromium content.
It is characterized by comprising a step of performing softening annealing at a temperature of 00°C or lower and 700°C or higher for less than 5 minutes, followed by descaling, cold rolling to reduce the thickness of the product plate, and final annealing. A method for producing cold-rolled chromium-based stainless steel sheets with excellent ridging resistance and press workability.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32376288A JPH02170923A (en) | 1988-12-23 | 1988-12-23 | Manufacture of cold rolled sheet of chromium stainless steel excellent in ridging resistance and press formability |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP32376288A JPH02170923A (en) | 1988-12-23 | 1988-12-23 | Manufacture of cold rolled sheet of chromium stainless steel excellent in ridging resistance and press formability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH02170923A true JPH02170923A (en) | 1990-07-02 |
Family
ID=18158341
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP32376288A Pending JPH02170923A (en) | 1988-12-23 | 1988-12-23 | Manufacture of cold rolled sheet of chromium stainless steel excellent in ridging resistance and press formability |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH02170923A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0499818A (en) * | 1990-08-15 | 1992-03-31 | Kawasaki Steel Corp | Production of high-purity ferritic stainless steel sheet having excellent brightness |
| EP1083237A3 (en) * | 1999-09-09 | 2003-11-05 | Kawasaki Steel Corporation | Ferritic Cr-containing steel sheet having excellent ductility, formability, and anti-ridging properties, and method of producing the same |
-
1988
- 1988-12-23 JP JP32376288A patent/JPH02170923A/en active Pending
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0499818A (en) * | 1990-08-15 | 1992-03-31 | Kawasaki Steel Corp | Production of high-purity ferritic stainless steel sheet having excellent brightness |
| EP1083237A3 (en) * | 1999-09-09 | 2003-11-05 | Kawasaki Steel Corporation | Ferritic Cr-containing steel sheet having excellent ductility, formability, and anti-ridging properties, and method of producing the same |
| KR100500791B1 (en) * | 1999-09-09 | 2005-07-12 | 제이에프이 스틸 가부시키가이샤 | FERRITIC Cr-CONTAINING STEEL SHEET HAVING EXCELLENT DUCTILITY, FORMABILITY, AND ANTI-RIDGING PROPERTIES, AND METHOD OF PRODUCING THE SAME |
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