JPH09256064A - Production of ferritic stainless steel thin sheet excellent in roping characteristic - Google Patents
Production of ferritic stainless steel thin sheet excellent in roping characteristicInfo
- Publication number
- JPH09256064A JPH09256064A JP6681096A JP6681096A JPH09256064A JP H09256064 A JPH09256064 A JP H09256064A JP 6681096 A JP6681096 A JP 6681096A JP 6681096 A JP6681096 A JP 6681096A JP H09256064 A JPH09256064 A JP H09256064A
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- Japan
- Prior art keywords
- stainless steel
- ferritic stainless
- rolling
- roping
- hot
- Prior art date
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- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、ローピング特性に
優れたフェライト系ステンレス鋼薄板の製造方法に関す
る。TECHNICAL FIELD The present invention relates to a method for producing a ferritic stainless steel sheet having excellent roping characteristics.
【０００２】[0002]
【従来の技術】フェライト系ステンレス鋼は、耐食性に
優れており、厨房用、自動車排気系材料用など多くの用
途に用いられている。近年では家電用に代表されるよう
に高加工性用材料としての用途が広がってきている。高
加工性材料には、深絞り性の指標として知られるｒ値が
高いことが求められ、このｒ値を向上させるためにＴ
ｉ，Ｎｂ等の炭窒化物形成元素を添加してＣ，Ｎを固定
した、いわゆるＩＦ系ステンレス鋼が用いられている。2. Description of the Related Art Ferritic stainless steel has excellent corrosion resistance and is used in many applications such as kitchen and automobile exhaust system materials. In recent years, its use as a material for high workability has been spreading, as represented by home appliances. Highly workable materials are required to have a high r value, which is known as an index of deep drawability, and in order to improve this r value, T
A so-called IF-based stainless steel in which carbon nitride forming elements such as i and Nb are added to fix C and N is used.
【０００３】またフェライト系ステンレス鋼の特徴とし
て表面の美麗さが挙げられる。表面特性を損なう欠陥と
しては、リジングと呼ばれる表面凹凸のうねりが良く知
られている。このリジングは、製品に成形加工等で１５
％程度の歪みを付与したときに現れる表面凹凸現象であ
り、その表面のうねりは圧延方向に伸び、通常５〜５０
μ程度のうねり高さである。Another characteristic of ferritic stainless steel is its beautiful surface. As a defect that impairs the surface characteristics, undulation of surface irregularities called ridging is well known. This ridging is 15
% Is a surface irregularity phenomenon that appears when a strain of about 5% is applied, and the waviness of the surface extends in the rolling direction and is usually 5 to 50.
The swell height is about μ.
【０００４】フェライトステンレス鋼において、リジン
グを防止するために種々の方策がこれまでに提案されて
いる。また、リジングのの発生メカニズムについても、
数多くの研究がなされており（例えば、鉄と鋼７６（１
９９０），Ｐ．１５２０参照）、リジング特性向上の手
法として、鋳造組織の微細化（等軸晶率の増加）、粗熱
延時の再結晶、γ相あるいはマルテンサイト相を用いた
圧延集合組織のランダム化等が有効であることが知られ
ている。In ferritic stainless steel, various measures have been proposed so far to prevent ridging. Also, regarding the mechanism of occurrence of ridging,
Numerous studies have been conducted (eg iron and steel 76 (1
990), p. 1520), refining the casting structure (increasing the equiaxed crystal ratio), recrystallization during rough hot rolling, and randomizing the rolling texture using the γ phase or martensite phase are effective methods for improving ridging characteristics. Is known to be.
【０００５】[0005]
【発明が解決しようとする課題】フェライト系ステンレ
ス鋼の表面欠陥としては、これまでリジングが問題視さ
れてきたが、最近ではフェライト系ステンレス鋼熱延板
を冷延したときに、冷延板の表面に発生した微小なうね
りが最終製品まで消えずに残り、微小なうねりであるけ
れども最近の厳しく求められる表面品位を満足すること
ができず、製品としての価値を損なうことが問題視され
ている。この微小なうねりは、冷延板の表面に高さ０．
２〜０．５μｍ程度で圧延方向に伸びたうねりであり、
このうねりは、リジングと区別してローピングと呼ばれ
ている。As a surface defect of ferritic stainless steel, ridging has been regarded as a problem so far, but recently, when cold rolling a ferritic stainless steel hot rolled sheet, The minute waviness that has occurred on the surface remains in the final product, and although it is a minute waviness, it is not possible to satisfy the recently demanded surface quality, and it is regarded as a problem that the value as a product is impaired. . The minute undulations have a height of 0.
The undulation extends in the rolling direction at about 2 to 0.5 μm,
This swell is called roping in distinction from ridging.
【０００６】これまではローピングはリジングと同一現
象として対策が検討されてきたが、リジングは発生しな
くてもローピングが発生するという事例も見られ、この
ローピングの軽減が重要な課題である。特に、高加工性
を有するＩＦ系フェライト系ステンレス鋼においてはロ
ーピング対策が求められる。Up to now, countermeasures have been studied on the assumption that roping is the same phenomenon as ridging, but there are cases where roping occurs even if ridging does not occur, and mitigating this roping is an important issue. In particular, IF-ferritic stainless steel having high workability requires measures against roping.
【０００７】そこで、本発明の目的は、特にＩＦ系フェ
ライトステンレス鋼において、その高加工性を確保しつ
つ、かつローピング特性に優れたフェライト系ステンレ
ス鋼薄板を、熱延板焼鈍なしに、生産性の高いプロセス
で製造する方法を提供することにある。Therefore, an object of the present invention is to improve productivity of a ferritic stainless steel thin plate excellent in roping characteristics while ensuring high workability, especially in IF ferritic stainless steel, without annealing the hot rolled sheet. It is to provide a method of manufacturing by a high process.
【０００８】[0008]
【課題を解決するための手段】本発明は、重量％で、 Ｃ ≦０．０１％、 Ｓｉ≦０．５％、 Ｍｎ≦０．５％、 Ｐ ≦０．０４％、 Ｓ ≦０．０１％、 Ｃｒ：１０〜２５％、 Ｔｉ：１０（Ｃ＋Ｎ）〜０．３％、 Ｎ ≦０．０１％ を含有し、残部がＦｅ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スラブを、１２５０℃以下に加熱
したのち、熱間圧延し、７５０℃以上で巻取った後、熱
延板焼鈍をすることなく、酸洗、冷延、冷延板焼鈍をす
ることを特徴とするローピング特性に優れたフェライト
系ステンレス鋼薄板の製造方法である。上記の熱間圧延
において、粗圧延の最終パス及びその前のパスの圧下率
をそれぞれ３０％以上とすることがローピング特性に優
れる。According to the present invention, in% by weight, C ≤ 0.01%, Si ≤ 0.5%, Mn ≤ 0.5%, P ≤ 0.04%, S ≤ 0.01 %, Cr: 10 to 25%, Ti: 10 (C + N) to 0.3%, N ≤ 0.01%, and the balance is Fe and unavoidable impurities. After being hot-rolled, it is hot-rolled and wound at 750 ° C. or higher, and then pickled, cold-rolled, and cold-rolled sheet is annealed without annealing the hot-rolled sheet. It is a method for manufacturing a ferritic stainless steel thin plate. In the above hot rolling, it is excellent in the roping property that the rolling reductions of the final pass of the rough rolling and the pass before the rough rolling are each 30% or more.
【０００９】上記フェライト系ステンレス鋼には、必要
により、さらにＢ ：０．０００５〜０．００５０％、
Ｚｒ：０．０１〜０．４％、Ｎｂ：０．０１〜０．４％
の内から１種以上を含有することも好適である。あるい
は、さらにＭｏ，Ｎｉ，Ｃｕの内から１種以上を０．０
２〜２．５％含有することも好適である。If necessary, the above ferritic stainless steel further contains B: 0.0005 to 0.0050%,
Zr: 0.01 to 0.4%, Nb: 0.01 to 0.4%
It is also preferable to contain one or more of the above. Alternatively, one or more of Mo, Ni and Cu may be further added to 0.0
It is also preferable to contain 2 to 2.5%.
【００１０】[0010]
【発明の実施の形態】以下に本発明を詳細に説明する。
まず、本発明のフェライト系ステンレス鋼の成分限定理
由について述べる。 Ｃ，Ｎ：Ｃ，Ｎは加工性を低下させる元素である。そこ
で高加工性（高ｒ値）を得るためには、Ｃ，Ｎを固定す
る必要があるけれども、Ｃ，Ｎが多すぎるとこれらを固
定するためのＴｉを多量に添加する必要があり、原料コ
ストを増加させる。また、Ｃ，Ｎを多量に含有すると、
冷延板焼鈍時に再結晶が遅延するために高温焼鈍が必要
となり、高温焼鈍に伴う種々の操業的問題が生じてく
る。したがって、Ｃ，Ｎ共に含有量は少ないが好まし
く、Ｃ，Ｎの上限をそれぞれ０．０１％とした。Ｃ量
は、できるだけ０．００５０％以下にすることが望まし
い。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below in detail.
First, the reasons for limiting the components of the ferritic stainless steel of the present invention will be described. C, N: C, N is an element that reduces workability. Therefore, in order to obtain high workability (high r value), it is necessary to fix C and N, but if C and N are too much, it is necessary to add a large amount of Ti to fix them. Increase costs. Moreover, when a large amount of C and N is contained,
Since recrystallization is delayed during cold-rolled sheet annealing, high-temperature annealing is required, which causes various operational problems associated with high-temperature annealing. Therefore, the contents of both C and N are preferably small, but the upper limits of C and N are set to 0.01%. It is desirable that the C content be 0.0050% or less as much as possible.
【００１１】Ｓｉ：Ｓｉは脱酸元素として必要である
が、多量の添加により降伏点の上昇を招くため、その上
限を０．５％とした。 Ｍｎ：Ｍｎも、Ｓｉと同様に脱酸元素であるが、多量の
添加により降伏点の上昇を招くため、その上限は０．５
％とした。本発明においてはスラブ加熱時に析出すると
考えられるＴｉの炭硫化物を安定化させるために、０．
１％程度とすることが好ましい。Si: Si is necessary as a deoxidizing element, but addition of a large amount causes an increase in the yield point, so the upper limit was made 0.5%. Mn: Mn is also a deoxidizing element like Si, but its upper limit is 0.5 because the addition of a large amount causes an increase in the yield point.
%. In the present invention, in order to stabilize Ti carbosulfide, which is considered to precipitate during slab heating,
It is preferably about 1%.
【００１２】Ｐ：Ｐは加工性を低下させる元素であるた
め、低い方が好ましい。したがってその上限は０．０４
％とした。 Ｓ：Ｓは加工性を低下させ、また多量に含有すると鋼の
脆化をもたらすため低い方が好ましく、その上限は０．
０１％とした。P: P is an element that lowers the workability, so its lower content is preferable. Therefore, the upper limit is 0.04
%. S: S lowers the workability, and when it is contained in a large amount, it causes the embrittlement of the steel, so the lower the S, the better.
01%.
【００１３】Ｃｒ：Ｃｒは含有量が１０％以下であると
ステンレス鋼の基本特性である耐食性が不足するためＣ
ｒ量の下限を１０％とした。一方、Ｃｒ量が多すぎる
と、高温巻取を行った場合にσ相などの金属間化合物が
析出して熱延板の靭性を劣化させるため、Ｃｒの上限は
２５％とした。原料コストを考慮すると１０〜１８％の
範囲とすることが好ましい。 Ｔｉ：Ｔｉは、Ｃ，Ｎを固定し、加工性を向上させる元
素である。ＴｉによるＣ，Ｎの固定を十分に行うととも
に、加工性（ｒ値）を向上させるためには、Ｔｉを１０
（Ｃ＋Ｎ）以上添加する。一方、Ｔｉを多量に添加する
と原料コストが増加し、また冷延時に表面疵が生じる等
の問題が起こるため、上限は０．３％とした。Cr: If the content of Cr is 10% or less, the corrosion resistance, which is a basic characteristic of stainless steel, is insufficient, so C
The lower limit of the amount of r was set to 10%. On the other hand, if the amount of Cr is too large, intermetallic compounds such as σ phase are precipitated when high temperature winding is carried out to deteriorate the toughness of the hot rolled sheet. Therefore, the upper limit of Cr was set to 25%. Considering the raw material cost, it is preferably in the range of 10 to 18%. Ti: Ti is an element that fixes C and N and improves workability. In order to sufficiently fix C and N with Ti and to improve workability (r value), Ti is set to 10
(C + N) or more is added. On the other hand, if a large amount of Ti is added, the raw material cost increases, and problems such as surface defects during cold rolling occur, so the upper limit was made 0.3%.
【００１４】Ｂ，Ｚｒ，Ｎｂ：本発明においては、必要
に応じて、さらに加工性を向上させるためにＢ，Ｚｒ，
Ｎｂの１種以上を添加する。その効果を得るためには、
Ｂは０．０００５％以上、Ｚｒは０．０１％以上、Ｎｂ
は０．０１％以上を添加する。しかし、添加量が多くな
ると、それぞれの加工性に及ぼす効果が飽和するばかり
でなく、原料コストの増加をもたらすため、Ｂは０．０
０５０％以下、Ｚｒは０．４％以下、Ｎｂは０．４％以
下とする。 Ｍｏ，Ｎｉ，Ｃｕ：本発明鋼の耐食性をさらに向上させ
るためには、Ｍｏ，Ｎｉ，Ｃｕを適宜添加する。Ｍｏ，
Ｎｉ，Ｃｕによる効果を有効に得るためには、それぞれ
０．０２％以上添加する。しかし、多量の添加は原料コ
ストを増加させるため、それぞれの添加量は２．５％以
下とする。B, Zr, Nb: In the present invention, in order to further improve the workability, B, Zr, Nb are used in the present invention.
Add one or more of Nb. To get that effect,
B is 0.0005% or more, Zr is 0.01% or more, Nb
Is added in an amount of 0.01% or more. However, when the addition amount increases, not only the effects on the respective workability become saturated, but also the raw material cost increases, so that B is 0.0
050% or less, Zr is 0.4% or less, and Nb is 0.4% or less. Mo, Ni, Cu: In order to further improve the corrosion resistance of the steel of the present invention, Mo, Ni, Cu are appropriately added. Mo,
In order to effectively obtain the effects of Ni and Cu, 0.02% or more of each is added. However, addition of a large amount increases the raw material cost, so the addition amount of each is 2.5% or less.
【００１５】次に、上記の本発明鋼を処理する熱間圧延
の条件について説明する。本発明者等は冷延後のローピ
ング特性に及ぼす冷延前の組織（再結晶率及び粒径）の
影響を調査した。表１に示す組成のフェライト系ステン
レス鋼を用いて冷延前の再結晶率を変化させ、圧下率８
０％の冷延をした後、圧延方向のローピング特性を調査
した。なお、未再結晶粒径は約３０００μｍであった。
図１にローピング特性と再結晶率及び再結晶粒径の関係
を示す。ローピングのランクは、Ａ：０．１５μｍ以
下、Ｂ：０．２５μｍ以下、Ｃ：０．３５μｍ以下、
Ｄ：０．３５μｍ超とした。ローピングのランクがＡま
たはＢランクであれば表面外観は合格と判定できる。そ
こで、図１よりローピング特性がＢランクとなる条件を
見てみると、約１００μｍ以下の再結晶粒径が約８０％
以上再結晶しているときであり、また、Ａランクとなる
条件は再結晶粒径が１００μｍ以下で再結晶率が約９０
％以上のときである。Next, the conditions of hot rolling for treating the above-described steel of the present invention will be described. The present inventors investigated the influence of the structure (recrystallization rate and grain size) before cold rolling on the roping characteristics after cold rolling. Using a ferritic stainless steel having the composition shown in Table 1, the recrystallization rate before cold rolling was changed to obtain a rolling reduction of 8
After 0% cold rolling, the roping characteristics in the rolling direction were investigated. The unrecrystallized grain size was about 3000 μm.
FIG. 1 shows the relationship between the roping characteristics and the recrystallization rate and the recrystallized grain size. The roping rank is A: 0.15 μm or less, B: 0.25 μm or less, C: 0.35 μm or less,
D: More than 0.35 μm. If the roping rank is A or B, the surface appearance can be judged to be acceptable. Therefore, looking at the condition where the roping characteristic is B rank from FIG. 1, the recrystallized grain size of about 100 μm or less is about 80%.
The above is the case of recrystallization, and the condition of rank A is that the recrystallized grain size is 100 μm or less and the recrystallization rate is about 90.
% Or more.
【００１６】そこで本発明者等は、熱延板において１０
０μｍ以下の再結晶粒径の再結晶率を８０％、あるいは
９０％以上とするための熱延条件について、表１に示す
組成のフェライト系ステンレス鋼を用いて調査した。そ
の結果、加熱温度を１２５０℃以下、巻取温度を７５０
℃以上としたときに熱延板の再結晶率は８０％以上とな
り、酸洗、冷延後のローピング特性はＢランクとなるこ
とが明らかになった。Therefore, the present inventors have made
The hot rolling conditions for setting the recrystallization rate of the recrystallized grain size of 0 μm or less to 80% or 90% or more were investigated using the ferritic stainless steel having the composition shown in Table 1. As a result, the heating temperature is 1250 ° C or lower, and the winding temperature is 750.
It was revealed that the recrystallization rate of the hot-rolled sheet was 80% or more when the temperature was higher than 0 ° C, and the roping property after pickling and cold rolling was B rank.
【００１７】[0017]
【表１】 [Table 1]
【００１８】熱延板焼鈍を施さない場合には熱延板の再
結晶率が高いほどローピング特性は向上する。巻取温度
が高いほど熱延板の再結晶率が高くなるのは言うまでも
ない。加熱温度が低いほど巻取時の再結晶が進行する原
因は、下記のように考えられる。再結晶は析出と競合し
たときには遅延することは知られている。加熱温度が低
いほど加熱時に析出物が多量に析出し（チタンの炭硫化
物であると考える）、再結晶抑制効果のある巻取時の析
出が少ないためと考えられる。また、熱延板の再結晶の
促進による細粒化により、冷延、焼鈍後のｒ値は高くな
る。析出物の安定化のためには加熱温度は低温ほど好ま
しく、１２００℃以下であることが望ましい。しかし、
加熱温度が低すぎると熱延疵が発生するため下限は１０
００℃とすることが好ましい。巻取温度は７５０℃以上
であれば熱延板の再結晶は進行するが、高すぎると再結
晶粒の粒成長をもたらし、ローピング特性は劣化するた
め、上限を８５０℃とすることが好ましい。When the hot-rolled sheet is not annealed, the higher the recrystallization rate of the hot-rolled sheet, the better the roping characteristics. It goes without saying that the higher the coiling temperature, the higher the recrystallization rate of the hot rolled sheet. The reason why the recrystallization during winding progresses as the heating temperature becomes lower is considered as follows. It is known that recrystallization is delayed when it competes with precipitation. It is considered that the lower the heating temperature is, the larger amount of precipitates are formed during heating (it is considered to be titanium carbosulfide), and there is less precipitation during winding, which has the effect of suppressing recrystallization. In addition, the r value after cold rolling and annealing increases due to the grain refinement due to the promotion of recrystallization of the hot rolled sheet. The heating temperature is preferably as low as possible to stabilize the precipitate, and is preferably 1200 ° C. or lower. But,
If the heating temperature is too low, thermal defects will occur, so the lower limit is 10
The temperature is preferably set to 00 ° C. If the coiling temperature is 750 ° C. or higher, recrystallization of the hot-rolled sheet proceeds, but if it is too high, recrystallized grains grow and the roping characteristics deteriorate, so the upper limit is preferably 850 ° C.
【００１９】また、本発明者らは、熱延板の再結晶率を
更に増加させるためには仕上げ圧延前の粒径微細化が有
効であることを見いだした。一般に再結晶は、初期粒径
が細粒であるほど速く進行することが知られている。仕
上げ圧延前の粗バーの再結晶粒径は約３００〜４００μ
ｍ、未再結晶粒径は約２０００〜４０００μｍであり、
未再結晶粒を少なくすること、すなわち粗バーでの再結
晶率を高めることが仕上げ圧延前の細粒化となる。粗バ
ーの再結晶率は９０％以上とすることで加熱温度１２５
０℃以下、巻取温度７５０℃以上の熱延板の再結晶率は
９０％以上となり、酸洗、冷延後のローピング特性はＡ
ランクとなる。The present inventors have also found that grain size refinement before finish rolling is effective for further increasing the recrystallization rate of the hot rolled sheet. It is generally known that recrystallization proceeds faster as the initial grain size becomes finer. The recrystallized grain size of the rough bar before finish rolling is about 300-400μ.
m, the unrecrystallized grain size is about 2000 to 4000 μm,
Reducing the number of unrecrystallized grains, that is, increasing the recrystallization rate in the coarse bar, results in grain refinement before finish rolling. The recrystallization rate of the coarse bar is set to 90% or more so that the heating temperature is 125
The recrystallization rate of the hot-rolled sheet at 0 ° C or lower and the coiling temperature of 750 ° C or higher is 90% or more, and the roping property after pickling and cold rolling is A.
It will be ranked.
【００２０】そこで本発明者等は粗バーの再結晶に及ぼ
す粗圧延条件の影響を調査した。その結果、粗バーの再
結晶に及ぼす影響としては歪の効果が大きく、特に粗圧
延パスの後段での歪（圧下率）の増加が再結晶進行に有
効であることを見いだした。さらに、粗バーの再結晶率
を９０％以上とするためには、加熱温度１２５０℃以下
のとき、粗圧延の最終パス及びその前のパスの圧下率を
それぞれ３０％以上とすることの有効性が明らかになっ
た。しかし、１パス当たりの圧下率は５０％以上となる
と熱延疵が発生することがあるため、５０％を上限とす
ることが好ましい。仕上げ圧延前に再結晶を促進し、細
粒化することにより、巻取時の再結晶が促進される。こ
のため冷延後のローピング特性及び冷延、焼鈍後のｒ値
が向上すると考えられる。Therefore, the present inventors investigated the effect of rough rolling conditions on the recrystallization of the rough bar. As a result, it was found that the effect of strain is large as an influence on the recrystallization of the rough bar, and that the increase of strain (reduction ratio) in the latter stage of the rough rolling pass is particularly effective for the progress of recrystallization. Further, in order to make the recrystallization rate of the coarse bar 90% or more, it is effective to set the reduction rate of the final pass of the rough rolling and the pass before it to 30% or more when the heating temperature is 1250 ° C. or less. Became clear. However, if the rolling reduction per pass is 50% or more, hot rolling may occur, so it is preferable to set 50% as the upper limit. By promoting recrystallization and fine-graining before finish rolling, recrystallization at the time of winding is promoted. Therefore, it is considered that the roping characteristics after cold rolling and the r value after cold rolling and annealing are improved.
【００２１】[0021]
【実施例】本発明の実施例を以下に示す。表２に示すフ
ェライト系ステンレス鋼１３種（Ａ〜Ｍ）を溶製し、鋳
片を熱間圧延する際に、加熱温度、粗圧延のパススケジ
ュールおよび巻取温度を変化させた。それらの条件を表
３に示す。なお、表中のＲf およびＲf-1 は、それぞれ
粗圧延最終パスの圧下率およびその前のパスの圧下率で
ある。次に、熱延板を焼鈍することなく、酸洗し、圧下
率８０％の冷延後、ローピング高さを測定した。ローピ
ング特性は、前述の評価ランクで評価し、ＡまたはＢラ
ンクを合格と判定した。Embodiments of the present invention will be described below. When 13 kinds (A to M) of ferritic stainless steel shown in Table 2 were melted and the slab was hot-rolled, the heating temperature, the rough rolling pass schedule and the winding temperature were changed. Table 3 shows those conditions. In addition, R f and R f-1 in the table are the rolling reduction of the final pass of rough rolling and the rolling reduction of the pass before that, respectively. Next, the hot rolled sheet was pickled without annealing, cold rolled at a rolling reduction of 80%, and the roping height was measured. The roping characteristics were evaluated by the above-mentioned evaluation rank, and the A or B rank was judged to be acceptable.
【００２２】さらに、冷延板は８７５℃で６０秒保定の
焼鈍をした後、引張試験片を採取し、ｒ値及びリジング
高さを測定した。ｒ値は、圧延方向から０，４５，９０
゜の角度で各２本採取した引張試験片を１５％引張後に
測定した。リジング高さは圧延方向に平行に１５％引張
後、うねりの高さを測定した（ｎ＝８）。リジングのラ
ンクは、Ａ：１０μｍ以下、Ｂ：２２μｍ以下、Ｃ：３
２μｍ以下、Ｄ：３２μｍ超とし、Ａ，Ｂランクを合格
と判定した。Further, the cold rolled sheet was annealed at 875 ° C. for 60 seconds and then a tensile test piece was sampled to measure the r value and the ridging height. r value is 0, 45, 90 from the rolling direction
Tensile test pieces, two each of which was taken at an angle of °, were measured after being stretched by 15%. The ridging height was measured by measuring the undulation height after pulling 15% parallel to the rolling direction (n = 8). The rank of ridging is A: 10 μm or less, B: 22 μm or less, C: 3
It was set to 2 μm or less and D: 32 μm or more, and the A and B ranks were judged to be acceptable.
【００２３】また、焼鈍板については、８０℃で１０％
硫酸溶液中の全面腐食試験を行い、耐食性を評価した。
評価は、腐食速度でランク付けし、Ａランク：４００ｇ
／ｍ2 ・ｈ以下、Ｂ：４０００ｇ／ｍ2 ・ｈ以下、Ｃ：
４０００ｇ／ｍ2 ・ｈ超とした。For the annealed sheet, 10% at 80 ° C
A general corrosion test was performed in a sulfuric acid solution to evaluate the corrosion resistance.
Evaluation is ranked by corrosion rate, A rank: 400g
/ M 2 · h or less, B: 4000 g / m 2 · h or less, C:
It was set to more than 4000 g / m 2 · h.
【００２４】各鋼種及び熱延条件とローピング、ｒ値、
リジングおよび耐食性の評価結果を表３に示す。本発明
の製造方法によって得られた鋼板は、ローピング特性、
ｒ値、リジング特性、耐食性ともに優れている。Each steel type, hot rolling conditions and roping, r value,
Table 3 shows the evaluation results of ridging and corrosion resistance. The steel sheet obtained by the manufacturing method of the present invention has roping characteristics,
Excellent in r-value, ridging property and corrosion resistance.
【００２５】[0025]
【表２】 [Table 2]
【００２６】[0026]
【表３】 [Table 3]
【００２７】[0027]
【発明の効果】本発明によるフェライト系ステンレス鋼
薄板の製造方法によれば、特にＣとＮの量に上限を規定
してＴｉを添加するとともに、熱間圧延時のスラブ加熱
温度と巻取温度、さらには粗圧延時に最終パスおよびそ
の前のパスの圧下率を下限規定することによって、耐ロ
ーピング特性に優れ、ｒ値およびリジング性も良好なフ
ェライト系ステンレス鋼薄板を得ることができる。さら
には、フェライト系ステンレス鋼薄板の製造において、
熱延板の焼鈍を省略できるので、生産性も改善されると
いう利点も得られる。According to the method for producing a ferritic stainless steel sheet according to the present invention, in particular, Ti is added with the upper limits of the amounts of C and N specified, and the slab heating temperature and coiling temperature during hot rolling are added. Further, by limiting the lower limit of the rolling reduction of the final pass and the pass before the rough rolling, it is possible to obtain a ferritic stainless steel thin plate having excellent roping resistance, r value and ridging property. Furthermore, in the production of ferritic stainless steel thin plates,
Since the annealing of the hot rolled sheet can be omitted, there is an advantage that the productivity is improved.
【図１】冷延前の組織（再結晶率、再結晶粒径）と冷延
後のローピングランクの関係を表す図である。FIG. 1 is a diagram showing a relationship between a structure before cold rolling (recrystallization rate, recrystallized grain size) and a roping rank after cold rolling.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 進藤 卓嗣 千葉県富津市新富20−１ 新日本製鐵株式 会社技術開発本部内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Takuji Shindo 20-1 Shintomi, Futtsu-shi, Chiba Nippon Steel Co., Ltd.
Claims (4)
ライト系ステンレス鋼スラブを、１２５０℃以下に加熱
したのち、熱間圧延し、７５０℃以上で巻取った後、熱
延板焼鈍をすることなく、酸洗、冷延、冷延板焼鈍をす
ることを特徴とするローピング特性に優れたフェライト
系ステンレス鋼薄板の製造方法。1. By weight%, C ≦ 0.01%, Si ≦ 0.5%, Mn ≦ 0.5%, P ≦ 0.04%, S ≦ 0.01%, Cr: 10 to 25% , Ti: 10 (C + N) to 0.3%, N ≦ 0.01%, and the balance ferritic stainless steel slab consisting of Fe and unavoidable impurities is heated to 1250 ° C. or lower, and then hot rolled. Then, after winding at 750 ° C. or higher, pickling, cold rolling, and cold-rolled sheet annealing are performed without hot-rolled sheet annealing, and a method for producing a ferritic stainless steel thin plate having excellent roping characteristics is characterized. .
びその前のパスの圧下率をそれぞれ３０％以上とするこ
とを特徴とする請求項１記載のローピング特性に優れた
フェライト系ステンレス鋼薄板の製造方法。2. The ferritic stainless steel thin plate excellent in roping characteristics according to claim 1, wherein, in hot rolling, the rolling reduction of the final pass of rough rolling and the pass before it are 30% or more, respectively. Manufacturing method.
または２記載のローピング特性に優れたフェライト系ス
テンレス鋼薄板の製造方法。3. A ferritic stainless steel further comprising one or more of B: 0.0005 to 0.0050%, Zr: 0.01 to 0.4%, and Nb: 0.01 to 0.4%. 1. The composition according to claim 1, wherein
Alternatively, the method for producing a ferritic stainless steel sheet having excellent roping characteristics according to the item 2.
ｏ，Ｎｉ，Ｃｕの内から１種以上を０．０２〜２．５％
含有するこを特徴とする請求項１，２または３のいずれ
かに記載のローピング特性に優れたフェライト系ステン
レス鋼薄板の製造方法。4. The ferritic stainless steel further comprises M
0.02 to 2.5% of one or more of o, Ni and Cu
The method for producing a ferritic stainless steel thin plate having excellent roping characteristics according to any one of claims 1, 2 and 3, characterized by containing.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6681096A JPH09256064A (en) | 1996-03-22 | 1996-03-22 | Production of ferritic stainless steel thin sheet excellent in roping characteristic |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6681096A JPH09256064A (en) | 1996-03-22 | 1996-03-22 | Production of ferritic stainless steel thin sheet excellent in roping characteristic |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH09256064A true JPH09256064A (en) | 1997-09-30 |
Family
ID=13326593
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6681096A Pending JPH09256064A (en) | 1996-03-22 | 1996-03-22 | Production of ferritic stainless steel thin sheet excellent in roping characteristic |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH09256064A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6855213B2 (en) | 1998-09-15 | 2005-02-15 | Armco Inc. | Non-ridging ferritic chromium alloyed steel |
| WO2012172808A1 (en) * | 2011-06-15 | 2012-12-20 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
| JP5168425B1 (en) * | 2011-06-15 | 2013-03-21 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
| KR20180068087A (en) * | 2016-12-13 | 2018-06-21 | 주식회사 포스코 | Ferritic stainless steel with improved impact toughness and method of manufacturing the same |
| JP2020532651A (en) * | 2017-08-31 | 2020-11-12 | ポスコＰｏｓｃｏ | Ferritic stainless steel with improved heat dissipation and workability and its manufacturing method |
-
1996
- 1996-03-22 JP JP6681096A patent/JPH09256064A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US6855213B2 (en) | 1998-09-15 | 2005-02-15 | Armco Inc. | Non-ridging ferritic chromium alloyed steel |
| WO2012172808A1 (en) * | 2011-06-15 | 2012-12-20 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
| JP5168425B1 (en) * | 2011-06-15 | 2013-03-21 | Ｊｆｅスチール株式会社 | Ferritic stainless steel |
| KR20180068087A (en) * | 2016-12-13 | 2018-06-21 | 주식회사 포스코 | Ferritic stainless steel with improved impact toughness and method of manufacturing the same |
| JP2020532651A (en) * | 2017-08-31 | 2020-11-12 | ポスコＰｏｓｃｏ | Ferritic stainless steel with improved heat dissipation and workability and its manufacturing method |
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