JPH10140292A - Manufacture of high purity ferritic stainless steel and steel sheet made of the steel - Google Patents
Manufacture of high purity ferritic stainless steel and steel sheet made of the steelInfo
- Publication number
- JPH10140292A JPH10140292A JP30261996A JP30261996A JPH10140292A JP H10140292 A JPH10140292 A JP H10140292A JP 30261996 A JP30261996 A JP 30261996A JP 30261996 A JP30261996 A JP 30261996A JP H10140292 A JPH10140292 A JP H10140292A
- Authority
- JP
- Japan
- Prior art keywords
- steel
- rolling
- ferritic stainless
- stainless steel
- hot
- 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.)
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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、加工性と耐ロ−ピ
ング性に優れた高純度フェライト系ステンレス鋼および
その鋼からなる鋼板を製造する方法に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a high-purity ferritic stainless steel excellent in workability and anti-rolling properties and a method for producing a steel sheet made of the steel.
【0002】[0002]
【従来の技術】鋼中のCとNの含有量を低減し、さらに
TiやNbの添加によりCやNの固定化を図ったフェラ
イト系ステンレス鋼(以下、高純度フェライト系ステン
レス鋼という)は、汎用鋼種であるSUS430鋼等に
比べて耐食性、加工性が良好である。そのため、高純度
フェライト系ステンレス鋼は、自動車排ガス用部材、化
学プラント用部材、および沿岸の建築物外装用部材等の
素材用として、生産量が増加している。2. Description of the Related Art Ferritic stainless steel (hereinafter, referred to as high-purity ferritic stainless steel) in which the contents of C and N in steel are reduced and C and N are fixed by adding Ti and Nb. It has better corrosion resistance and workability than SUS430 steel, which is a general-purpose steel type. Therefore, the production of high-purity ferritic stainless steel has been increasing as a material for automobile exhaust gas members, chemical plant members, and coastal building exterior members.
【0003】通常、高純度フェライト系ステンレス鋼板
は、連続鋳造−熱間圧延−熱延板焼鈍−酸洗−冷間圧延
(1または2回)−仕上げ焼鈍−酸洗の工程によって生産
されている。連続焼鈍設備により行われる熱延板焼鈍
は、IF鋼(InterstitialFree 鋼板)や低炭素鋼板
を製造する際には行うことがない、ステンレス鋼板を製
造する際の特有の工程である。[0003] Usually, a high-purity ferritic stainless steel sheet is continuously cast, hot-rolled, hot-rolled sheet annealing, pickling and cold rolling.
(1 or 2 times)-Finish annealing-Pickling. The hot-rolled sheet annealing performed by the continuous annealing equipment is a specific process for manufacturing a stainless steel sheet, which is not performed when manufacturing an IF steel (Interstitial Free steel sheet) or a low carbon steel sheet.
【0004】高純度フェライト系ステンレス鋼板を、I
F鋼板や低炭素鋼板を製造する際に用いる設備、すなわ
ち、熱延板焼鈍を行わない通常の設備で製造することが
できれば、生産性を顕著に上げることができる。A high-purity ferritic stainless steel sheet is
If it can be manufactured with equipment used when manufacturing F steel sheets and low carbon steel sheets, that is, ordinary equipment that does not perform hot-rolled sheet annealing, productivity can be significantly increased.
【0005】しかし、今日まで知られている技術では、
熱延板焼鈍の工程を省略して高純度フェライト系ステン
レス鋼板を製造することはできなかった。それは主に以
下の2つの理由による。[0005] However, in the techniques known to date,
A high-purity ferritic stainless steel sheet could not be manufactured by omitting the hot-rolled sheet annealing step. It is mainly due to the following two reasons.
【0006】耐ローピング性の低下 高純度フェライト系ステンレス鋼の冷延板を目的の形状
に加工するために冷間圧延方向に引張変形力を加える
と、ロ−ピングと呼ばれる圧延方向に平行のしわ状の欠
陥が生じることがある。ロ−ピングの原因は、熱間圧延
により圧延方向に著しく伸びた結晶粒(以後、バンド組
織と称する)が冷間圧延後の仕上げ焼鈍の際に再結晶化
して結晶方位の近い粒の集団を形成するためとされてい
る。バンド組織が生じた高純度フェライト系ステンレス
鋼に対しては、通常、熱間圧延後に熱延板焼鈍を施して
バンド組織を破壊している。熱延板焼鈍を行わなけれ
ば、バンド組織が残留するので、冷延板を加工した際に
ロ−ピングが発生する。When a tensile deformation force is applied in the cold rolling direction in order to process a cold-rolled sheet of high-purity ferritic stainless steel into a desired shape, wrinkles parallel to the rolling direction called roping are obtained. Defects may occur. The cause of the rolling is that the crystal grains (hereinafter, referred to as band structure) remarkably elongated in the rolling direction by hot rolling are recrystallized at the time of finish annealing after cold rolling to form a group of grains having crystal orientations close to each other. It is supposed to form. For a high-purity ferritic stainless steel having a band structure, hot band rolling is usually performed after hot rolling to break the band structure. If the hot-rolled sheet annealing is not performed, the band structure remains, so that the rolling occurs when the cold-rolled sheet is processed.
【0007】伸びの低下 熱延板焼鈍を行わなければ、フェライト系ステンレス鋼
の冷延板の伸び(特に圧延方向から90度)が著しく低下
する。バンド組織の残留や微細な析出物の存在に起因す
る延性不足が原因であると考えられる。Unless the hot-rolled sheet is annealed, the elongation (particularly 90 degrees from the rolling direction) of the cold-rolled sheet of ferritic stainless steel is remarkably reduced. This is considered to be due to insufficient ductility due to the residual band structure and the presence of fine precipitates.
【0008】熱延板焼鈍を省略しても加工性と耐ロ−ピ
ング性が劣化しない高純度フェライト系ステンレス鋼板
の製造方法として、特開昭59-13026号公報、特開昭62-1
99721号公報、特開昭62-77423 号公報等に熱間圧延の粗
圧延後のパス間時間を通常より長くしてバンド組織を破
壊する方法が開示されている。しかし、この方法では、
粗圧延ロール後段での圧下率を高くする必要があるので
製品の表面にスケール疵等の表面疵が多く発生してしま
う。[0008] As a method for producing a high-purity ferritic stainless steel sheet in which the workability and the rolling resistance do not deteriorate even if the hot-rolled sheet annealing is omitted, JP-A-59-13026 and JP-A-62-1
JP-A-99721 and JP-A-62-77423 disclose methods for breaking the band structure by making the time between passes after rough rolling in hot rolling longer than usual. But with this method,
Since it is necessary to increase the rolling reduction in the subsequent stage of the rough rolling roll, many surface flaws such as scale flaws are generated on the surface of the product.
【0009】[0009]
【発明が解決しようとする課題】上記のように、熱延板
焼鈍を省略して、高純度フェライト系ステンレス鋼板を
製造することは困難であった。本発明の目的は、冷延板
を製造する際に熱延板焼鈍を施さなくとも加工性と耐ロ
ーピング性を兼ね備えた冷延板が得られる高純度フェラ
イト系ステンレス鋼、および優れた加工性と耐ロ−ピン
グ性を有する高純度フェライト系ステンレス鋼板を製造
する方法を提供することである。As described above, it has been difficult to manufacture a high-purity ferritic stainless steel sheet by omitting the hot-rolled sheet annealing. An object of the present invention is to provide a high-purity ferritic stainless steel capable of obtaining a cold-rolled sheet having both workability and roping resistance without performing hot-rolling sheet annealing when manufacturing a cold-rolled sheet, and excellent workability. An object of the present invention is to provide a method for producing a high-purity ferritic stainless steel sheet having a resistance to rolling.
【0010】[0010]
【課題を解決するための手段】本発明の要旨は、下記の
高純度フェライト系ステンレス鋼(以下、本発明鋼とも
いう。)およびその鋼からなる鋼板の製造方法にある。SUMMARY OF THE INVENTION The gist of the present invention resides in the following high-purity ferritic stainless steel (hereinafter also referred to as the present invention steel) and a method for producing a steel sheet made of the steel.
【0011】以下の説明において、各元素の含有量の%
表示は重量%を意味する。In the following description, the percentage of the content of each element
The indication means% by weight.
【0012】1.本発明の高純度フェライト系ステンレ
ス鋼 『C:0.005%以下、Si:0.05〜1%、M
n:0.05〜1%、P:0.03%以下、S:0.0
1%以下、Ni:0〜1%、Cr:13〜20%、M
o:0〜2%、Cu:0〜1%、V:0〜1%、N:
0.02%以下、Ti*:30×C(%)以上、0.2
%以下、を含有し、残部はFeおよび不可避的不純物か
らなる。1. High purity ferritic stainless steel of the present invention [C: 0.005% or less, Si: 0.05 to 1%, M
n: 0.05-1%, P: 0.03% or less, S: 0.0
1% or less, Ni: 0 to 1%, Cr: 13 to 20%, M
o: 0 to 2%, Cu: 0 to 1%, V: 0 to 1%, N:
0.02% or less, Ti * : 30 × C (%) or more, 0.2
% Or less, with the balance being Fe and unavoidable impurities.
【0013】ただし、Ti*は下式で表されるものとす
る。However, Ti * is represented by the following equation.
【0014】Ti*=全Ti(%)−(48/14)×
N(%)』 2.本発明の高純度フェライト系ステンレス鋼板の製造
方法。Ti * = Total Ti (%)-(48/14) ×
N (%)] 2. A method for producing a high-purity ferritic stainless steel sheet according to the present invention.
【0015】『上記1に記載する鋼に、仕上温度が85
0〜1000℃である熱間圧延を施した後、700℃以
上の温度で巻き取り、さらに、圧下率55〜70%の冷
間圧延を施す。』 本発明鋼は、下記に規定する化学組成を有するので、冷
延板を製造する工程中に熱延板焼鈍を施さなくとも加工
性と耐ローピング性を兼ね備えている。特にCの含有量
を0.005%以下、Tiの含有量をTi*で換算して
30×C(%)以上0.2%以下{ただし、Ti*は、
全Ti(%)−(48/14)×N(%)で定義される
ものであり、以下、有効Ti量ともいう。}に規定する
ことで耐ローピング性と加工性を向上させている。"The steel described in 1 above has a finishing temperature of 85
After performing hot rolling at 0 to 1000 ° C., winding is performed at a temperature of 700 ° C. or higher, and further, cold rolling is performed at a draft of 55 to 70%. Since the steel of the present invention has the chemical composition defined below, it has both workability and roping resistance without performing hot-rolled sheet annealing during the process of manufacturing a cold-rolled sheet. Especially below 0.005% content of C, and converting the content of Ti in Ti * 30 × C (%) 0.2% or less {However, Ti * is
Total Ti (%)-(48/14) x N (%), which is also referred to as effective Ti amount below. By specifying in}, the roping resistance and workability are improved.
【0016】[0016]
(1)化学組成 以下、各元素の作用と含有量および含有量を規定した理
由について述べる。(1) Chemical Composition Hereinafter, the action, the content of each element and the reason for defining the content will be described.
【0017】C:Cは、耐食性や加工性を劣化させるの
で極力低減するのが好ましい。含有量が0.005%を
超えると、耐ロ−ピング性が悪化する。したがって、C
の含有量を0.005%以下とした。C: Since C deteriorates corrosion resistance and workability, it is preferable to reduce C as much as possible. If the content exceeds 0.005%, the anti-rolling property deteriorates. Therefore, C
Was made 0.005% or less.
【0018】Si:Siは、鋼の脱酸に必要な元素であ
り、少なくとも0.05%以上は含有させる必要があ
る。しかし、1%を超えて含有させると、加工性が著し
く悪化してしまう。したがって、Siの含有量を0.0
5〜1%とした。Si: Si is an element necessary for deoxidizing steel, and it is necessary to contain at least 0.05% or more. However, when the content exceeds 1%, the workability is remarkably deteriorated. Therefore, the content of Si is set to 0.0
It was set to 5-1%.
【0019】Mn:Mnは、鋼の脱酸、脱硫に必要な元
素であり、少なくとも0.05%以上は含有させる必要
がある。しかし、1%を超えて含有させると加工性が著
しく悪化してしまう。したがって、Mnの含有量を0.
05〜1%とした。Mn: Mn is an element required for deoxidation and desulfurization of steel, and must be contained at least 0.05% or more. However, when the content exceeds 1%, the workability is remarkably deteriorated. Therefore, the content of Mn is set to 0.1.
05 to 1%.
【0020】P、S:PおよびSは、熱間加工性と靱性
を著しく悪化させるので含有量を極力低減することが望
ましい。PとSをそれぞれ0.03%、0.01%を超
えて含有させると靱性が著しく悪化する。したがって、
Pの含有量の上限は0.03%、Sの含有量の上限は
0.01%とした。P, S: Since P and S significantly deteriorate hot workability and toughness, it is desirable to reduce the content as much as possible. If P and S are contained in excess of 0.03% and 0.01%, respectively, the toughness is remarkably deteriorated. Therefore,
The upper limit of the P content was 0.03%, and the upper limit of the S content was 0.01%.
【0021】Ni、Mo、Cu、V:これらの元素は、
耐食性を向上させる元素であり、必要に応じて添加する
ことが望ましい。その効果を得るためには、Niは0.
3%、Moは0.5%、Cuは0.3%、Vは0.3%
以上含有させるのが好ましい。しかし過剰に含有させる
と鋼を硬質化させるのでその上限をNi、CuおよびV
は1%、Moは2%とした。前記上限の好ましいのは、
Ni、Cu、Vは0.5%、Moは1.5%である。Ni, Mo, Cu, V: These elements are
It is an element that improves corrosion resistance, and is desirably added as necessary. In order to obtain the effect, Ni should be contained in an amount of 0.1.
3%, Mo is 0.5%, Cu is 0.3%, V is 0.3%
It is preferable to contain the above. However, if contained excessively, it hardens the steel, so the upper limit is Ni, Cu and V.
Was 1% and Mo was 2%. Preferably, the upper limit is
Ni, Cu, and V are 0.5% and Mo is 1.5%.
【0022】Cr:Crは、鋼の耐食性を担う重要な元
素であり、13%以上含有させる必要がある。しかしな
がら、過剰に添加すると鋼を硬質化し、加工性を低下さ
せるので、その上限を20%とした。Cr: Cr is an important element that contributes to the corrosion resistance of steel, and it is necessary to contain 13% or more. However, an excessive addition hardens the steel and lowers the workability, so the upper limit was made 20%.
【0023】N:Nは、Cと同様、耐食性、加工性を劣
化させるので、極力低減することが好ましい。0.02
%を超えると加工性が著しく劣化するので上限を0.0
2%とした。N: N, like C, deteriorates corrosion resistance and workability, so it is preferable to reduce N as much as possible. 0.02
%, The workability is remarkably deteriorated.
2%.
【0024】Ti:Tiは、CやNと安定な炭窒化物を
形成し、鋼の加工性を著しく向上させる最も重要な元素
である。Tiは特にNとの親和力が強く、凝固過程でほ
ぼ全量のNがTiにより固定される。有効Ti量すなわ
ちTi*(全Ti量からTiNとして析出したTiを差
し引いたTi量)が30×C(%)よりも低い場合は、
CはTiにより完全に固定されずr値は低下する。一
方、Ti*が0.2%を超えると熱延中に再結晶化が抑
制され、冷延板の耐ローピング性を悪化させる。よっ
て、Ti*を30×C(%)以上、0.2%以下とし
た。Ti: Ti is the most important element that forms stable carbonitrides with C and N and significantly improves the workability of steel. Ti has a particularly strong affinity for N, and almost the entire amount of N is fixed by Ti during the solidification process. When the effective Ti amount, that is, Ti * (the Ti amount obtained by subtracting Ti precipitated as TiN from the total Ti amount) is lower than 30 × C (%),
C is not completely fixed by Ti, and the r value decreases. On the other hand, if Ti * exceeds 0.2%, recrystallization is suppressed during hot rolling, and the roping resistance of the cold rolled sheet is deteriorated. Therefore, the content of Ti * is set to 30 × C (%) or more and 0.2% or less.
【0025】(2)製造方法 本発明の方法で高純度フェライト系ステンレス鋼板を製
造すれば、より加工性に優れた冷延板を製造することが
できる。(2) Manufacturing Method If a high-purity ferritic stainless steel sheet is manufactured by the method of the present invention, a cold-rolled sheet having more excellent workability can be manufactured.
【0026】本発明のフェライト系ステンレス鋼板の製
造方法では、まず、本発明で規定する化学組成の鋼に熱
間圧延を施す。その際の仕上げ温度、すなわち熱間圧延
直後の材料の温度を850℃〜1000℃となるよう
に、熱間圧延温度を調整する。その後、熱延板の温度が
あまり低下しないうちに、700℃以上を保ったまま巻
き取る。巻き取り温度の上限については、特に規定する
必要はなく、設備の構造上耐えうる温度で構わない。仕
上げ温度および巻き取り温度をこの温度に規定すること
により、冷延板を所望の形状に成形する際の加工性が向
上する。これは、圧延方向から90度の方向のr値(以
下、r90値という)が向上するためである。r90値が向
上する要因は、熱間加工後から巻き取りまでの間に鋼板
中で回復が進行し熱延板が軟質化するため、冷延集合組
織が低圧下側にシフトしr90値が向上する再結晶集合組
織が形成されるためである。In the method for producing a ferritic stainless steel sheet according to the present invention, first, steel having the chemical composition specified in the present invention is subjected to hot rolling. The hot rolling temperature is adjusted so that the finishing temperature at that time, that is, the temperature of the material immediately after hot rolling is 850 ° C. to 1000 ° C. Thereafter, before the temperature of the hot-rolled sheet is not significantly reduced, the hot-rolled sheet is wound while maintaining the temperature at 700 ° C. or higher. The upper limit of the winding temperature does not need to be particularly specified, and may be a temperature that can withstand the structure of the equipment. By setting the finishing temperature and the winding temperature to these temperatures, workability in forming the cold-rolled sheet into a desired shape is improved. This is the direction of the r value of 90 degrees from the rolling direction (hereinafter, referred to as r 90 value) in order to improve. Factors r 90 value is improved, in order to soften the hot rolled plate proceeds and recover steel sheet until winding after hot working, cold-rolled texture is shifted to a low pressure side r 90 value This is because a recrystallized texture in which is improved is formed.
【0027】冷間圧延の圧下率も冷延板を目的の形状に
加工する際の伸びとr値に影響を及ぼす。圧下率が55
%未満では、集合組織があまり発達せず、良好なr値が
得られない。一方、圧下率が70%を超えるとr90値と
伸びが低下する場合がある。したがって、圧下率の範囲
を55%〜70%とするのが望ましい。The rolling reduction of the cold rolling also affects the elongation and r-value when the cold-rolled sheet is processed into a desired shape. Reduction rate 55
If it is less than%, the texture does not develop much, and a good r value cannot be obtained. On the other hand, if the reduction rate is lowered r 90 value and elongation exceeds 70%. Therefore, it is desirable to set the range of the rolling reduction to 55% to 70%.
【0028】[0028]
【発明の実施の形態】本発明の高純度フェライト系ステ
ンレス鋼を用いて、高純度フェライト系ステンレス鋼板
を製造する工程を具体的に説明する。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS A process for producing a high-purity ferritic stainless steel sheet using the high-purity ferritic stainless steel of the present invention will be specifically described.
【0029】本発明で規定する化学組成の高純度フェラ
イト系ステンレス鋼に熱間圧延を施す。熱間圧延前の工
程としては、本発明で規定する化学組成となるように、
真空脱炭法で溶製し、連続鋳造によりスラブに加工する
のが好ましい。熱間圧延は何ら特殊なものでなく、通常
の熱間圧延設備を使用することができる。熱間圧延後に
熱延板焼鈍は行わない。熱間圧延後に脱スケールを目的
とする通常の酸洗処理を施しても構わない。本発明で規
定する化学組成を有する鋼は、熱延粗圧延後のパス間で
再結晶が起こり、熱間圧延で発生したバンド組織が破壊
される。したがって、冷延板を加工した際にローピング
が発生しない。このように、熱間圧延後にバンド組織を
破壊するための熱延板焼鈍を施す必要がない。次の工程
として、熱延板に冷間圧延を施す。冷間圧延は何ら特殊
なものでなく、通常の冷間圧延装置を使用することがで
きる。The high-purity ferritic stainless steel having the chemical composition specified in the present invention is subjected to hot rolling. As a process before hot rolling, so that the chemical composition specified in the present invention,
It is preferable to melt by a vacuum decarburization method and process it into a slab by continuous casting. Hot rolling is not special, and ordinary hot rolling equipment can be used. No hot-rolled sheet annealing is performed after hot rolling. After hot rolling, a normal pickling treatment for the purpose of descaling may be performed. In the steel having the chemical composition specified in the present invention, recrystallization occurs between passes after hot rolling rough rolling, and the band structure generated by hot rolling is destroyed. Therefore, no roping occurs when the cold rolled sheet is processed. Thus, there is no need to perform hot-rolled sheet annealing for breaking the band structure after hot rolling. In the next step, the hot-rolled sheet is subjected to cold rolling. Cold rolling is not special, and a normal cold rolling device can be used.
【0030】冷間圧延後の工程としては、軟質化させる
ために通常の仕上げ焼鈍を行うのが望ましい。さらに、
仕上げ焼鈍後に脱スケールを目的とする通常の酸洗処理
を行うのが望ましい。上記した製造工程により、加工性
と耐ローピング性を有する高純度フェライト系ステンレ
ス鋼板を製造することができる。As a process after the cold rolling, it is desirable to perform normal finish annealing in order to soften. further,
It is desirable to perform a normal pickling treatment for the purpose of descaling after the finish annealing. By the above-described manufacturing process, a high-purity ferritic stainless steel sheet having workability and roping resistance can be manufactured.
【0031】上記の熱間圧延の仕上げ温度を850〜1
000℃となるように調整し、熱間圧延直後に通常の巻
き取り装置を使用して、熱延板の温度を700℃以上に
保ったまま巻き取りを行って、圧下率が55〜70%の
冷間圧延を施すことにより、さらに加工性に優れた高純
度フェライト系ステンレス鋼板を製造することができ
る。The finishing temperature of the hot rolling is set to 850 to 1
The temperature was adjusted to 000 ° C., and immediately after hot rolling, using a normal winding device, the hot rolled sheet was wound while keeping the temperature at 700 ° C. or higher, and the rolling reduction was 55 to 70%. By performing the cold rolling, a high-purity ferritic stainless steel sheet having more excellent workability can be produced.
【0032】ここでいう圧下率とは、{(冷間圧延前の
板厚−冷間圧延後の板厚)/(冷間圧延前の板厚)}×
100で定義されるものである。なお、冷間圧延は2回
行っても構わない。その際の圧下率は、{(1回目の冷
間圧延前の板厚−2回目の冷間圧延後の板厚)/(1回
目の冷間圧延前の板厚)}×100で定義される。The rolling reduction here means {(sheet thickness before cold rolling-sheet thickness after cold rolling) / (sheet thickness before cold rolling)} ×
It is defined by 100. Note that cold rolling may be performed twice. The rolling reduction at that time is defined as {(sheet thickness before first cold rolling—thickness after second cold rolling) / (sheet thickness before first cold rolling)} × 100. You.
【0033】[0033]
【実施例】表1に示す様々な化学組成の高純度フェライ
ト系ステンレス鋼を真空溶解法により溶製し、50kg
インゴットに鋳造した。つぎに、分塊圧延により板厚4
0mmのスラブとし、1150℃で1時間均熱した後
に、ワ−クロ−ル径500mmの1スタンド−2Hiの
熱間圧延ミルを使用して熱間圧延を7パス施して板厚4
mmの熱延板に形成した。その際の仕上温度は、700
〜900℃とした。熱間圧延後の熱延板を空冷した後、
500〜800℃の様々な巻き取り温度で巻き取った。
巻き取り後の熱延板は、50℃/hの冷却速度で徐冷し
た。EXAMPLE High-purity ferritic stainless steels of various chemical compositions shown in Table 1 were melted by the vacuum melting method, and 50 kg
Cast into ingot. Next, the sheet thickness of 4
After forming a slab of 0 mm and soaking at 1150 ° C. for 1 hour, 7 passes of hot rolling were performed using a 1-stand-2Hi hot rolling mill having a work-roll diameter of 500 mm to obtain a sheet thickness of 4 mm.
mm hot-rolled sheet. The finishing temperature at that time is 700
~ 900 ° C. After air-cooling the hot-rolled sheet after hot rolling,
Winding was performed at various winding temperatures of 500-800C.
The rolled hot rolled sheet was gradually cooled at a cooling rate of 50 ° C./h.
【0034】次にワ−クロ−ル径が150mmで4Hi
の冷間圧延ミルを使用して圧下率が50〜80%の冷間
圧延を施して高純度フェライト系ステンレス鋼板を製造
した。その後、950℃で1.5分間保持する通常の仕
上焼鈍を施した。Next, when the work roll diameter is 150 mm and 4Hi
Was subjected to cold rolling at a reduction ratio of 50 to 80% using a cold rolling mill of No. 1 to produce a high-purity ferritic stainless steel sheet. Thereafter, normal finish annealing at 950 ° C. for 1.5 minutes was performed.
【0035】[0035]
【表1】 [Table 1]
【0036】次に、上記工程で製造した冷延板の加工性
と耐ローピング性を調査した。Next, the workability and roping resistance of the cold rolled sheet manufactured in the above process were investigated.
【0037】加工性については、圧延方向から90度の
方向となるように、冷延板からJIS13B号試験片を
採取し、引張試験を行うことにより評価した。圧延方向
から90度の方向に試験片を切り出すのは、この方向が
最も製造条件の影響を受けやすいことや製品板のミルシ
ートに90度方向の伸びを記載するためである。また、
r値の評価が不要な理由は、熱延板焼鈍の省略によりr
値が著しく低下することはないためである。The workability was evaluated by taking a JIS No. 13B test piece from the cold-rolled sheet so as to be 90 degrees from the rolling direction and performing a tensile test. The reason why the test piece is cut in a direction at 90 degrees from the rolling direction is that this direction is most susceptible to the manufacturing conditions and that the elongation in the direction of 90 degrees is described on the mill sheet of the product plate. Also,
The reason that the evaluation of the r value is unnecessary is that the omission of the hot-rolled sheet annealing
This is because the value does not significantly decrease.
【0038】一方、耐ロ−ピング性ついては、圧延方向
に平行となるように、冷延板からJIS5号試験片を採
取した後、冷延板の両面を鏡面研磨し、20%の引張歪
みを付与して発生するローピングを測定することにより
評価した。On the other hand, regarding the anti-rolling property, a JIS No. 5 test piece was sampled from a cold-rolled sheet so as to be parallel to the rolling direction, and both sides of the cold-rolled sheet were mirror-polished to reduce a tensile strain of 20%. It was evaluated by measuring the roping that occurred upon application.
【0039】加工性については、30%以上の伸びを示
した冷延板を伸びが良好で加工性に優れる鋼板と評価し
た。30%未満の伸びの冷延板では、ユーザーがそれを
プレスした場合に割れが生じる可能性が高くなる。耐ロ
ーピング性については、表2で示すように、ローピング
高さが40μm未満、すなわちB’以上の評価を有する
冷延板を優れた耐ローピング性を持つ鋼板と評価した。
40μm以上の高さのローピングを有する冷延板は、プ
レス後に研磨等によりにしわを除去する必要がある。With respect to workability, a cold rolled sheet having an elongation of 30% or more was evaluated as a steel sheet having good elongation and excellent workability. A cold rolled sheet with an elongation of less than 30% is more likely to crack when the user presses it. Regarding roping resistance, as shown in Table 2, a cold-rolled sheet having a roping height of less than 40 μm, that is, a rating of B ′ or more was evaluated as a steel sheet having excellent roping resistance.
For a cold rolled sheet having a roping of a height of 40 μm or more, it is necessary to remove wrinkles by polishing or the like after pressing.
【0040】[0040]
【表2】 [Table 2]
【0041】測定結果を表3に示した。Table 3 shows the measurement results.
【0042】[0042]
【表3】 [Table 3]
【0043】表3より、本発明の高純度フェライト系ス
テンレス鋼(A〜F)は、耐ローピング性がB’以上で
伸びが30%以上であり、耐ローピング性と加工性に優
れていることがわかる。一方、本発明で規定する化学組
成から外れている鋼(1〜4)は、耐ローピング性か加
工性のいずれか、もしくは両方の性能が、本発明鋼より
も劣っていることが分かる。From Table 3, it can be seen that the high-purity ferritic stainless steels (A to F) of the present invention have a roping resistance of B 'or more and an elongation of 30% or more, and are excellent in roping resistance and workability. I understand. On the other hand, it can be seen that steels (1 to 4) deviating from the chemical composition defined in the present invention are inferior to the steel of the present invention in either or both roping resistance and workability.
【0044】また、本発明方法で規定する熱間圧延、巻
き取りおよび冷間圧延(表3では*で示した)を施して
製造した鋼板は、本発明の方法で規定する範囲外の方法
で製造した鋼板よりも、ほぼ同じ化学組成の鋼同士で比
較した場合に、大きな伸びを示し、加工性がより優れて
いることが分かる。Further, the steel sheet produced by performing the hot rolling, winding and cold rolling (indicated by * in Table 3) specified by the method of the present invention is performed by a method outside the range specified by the method of the present invention. Compared to steel sheets having substantially the same chemical composition as compared to the manufactured steel sheets, the steel sheets show a large elongation, indicating that the workability is more excellent.
【0045】[0045]
【発明の効果】本発明のフェライト系ステンレス鋼は、
冷延板を製造する際に熱延板焼鈍を施さなくとも耐ロー
ピング性と加工性に優れるという特性を持っている。さ
らに、本発明方法で得られる鋼板は、さらに優れた耐ロ
ーピング性と加工性を持っている。The ferritic stainless steel of the present invention
It has the property of being excellent in roping resistance and workability even if hot rolled sheet annealing is not performed when manufacturing a cold rolled sheet. Furthermore, the steel sheet obtained by the method of the present invention has more excellent roping resistance and workability.
Claims (2)
0.05〜1%、Mn:0.05〜1%、P:0.03
%以下、S:0.01%以下、Ni:0〜1%、Cr:
13〜20%、Mo:0〜2%、Cu:0〜1%、V:
0〜1%、N:0.02%以下、Ti*:30×C
(%)以上0.2%以下を含有し、残部はFeおよび不
可避的不純物からなる高純度フェライト系ステンレス
鋼。ただし、Ti*は下式で表されるものとする。 Ti*=全Ti(%)−(48/14)×N(%)(1) C: 0.005% or less by weight, Si:
0.05-1%, Mn: 0.05-1%, P: 0.03
%, S: 0.01% or less, Ni: 0 to 1%, Cr:
13-20%, Mo: 0-2%, Cu: 0-1%, V:
0 to 1%, N: 0.02% or less, Ti * : 30 × C
High purity ferritic stainless steel containing at least (%) and at most 0.2%, with the balance being Fe and unavoidable impurities. Here, Ti * is represented by the following equation. Ti * = Total Ti (%)-(48/14) × N (%)
温度が850〜1000℃である熱間圧延を施した後、
700℃以上の温度で巻き取り、さらに、圧下率55〜
70%の冷間圧延を施すことを特徴とする高純度フェラ
イト系ステンレス鋼板の製造方法。2. A steel having the chemical composition according to claim 1, which is subjected to hot rolling at a finishing temperature of 850 to 1000 ° C.,
Winding at a temperature of 700 ° C. or more
A method for producing a high-purity ferritic stainless steel sheet, comprising performing 70% cold rolling.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP30261996A JPH10140292A (en) | 1996-11-14 | 1996-11-14 | Manufacture of high purity ferritic stainless steel and steel sheet made of the steel |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP30261996A JPH10140292A (en) | 1996-11-14 | 1996-11-14 | Manufacture of high purity ferritic stainless steel and steel sheet made of the steel |
Publications (1)
Publication Number | Publication Date |
---|---|
JPH10140292A true JPH10140292A (en) | 1998-05-26 |
Family
ID=17911172
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP30261996A Pending JPH10140292A (en) | 1996-11-14 | 1996-11-14 | Manufacture of high purity ferritic stainless steel and steel sheet made of the steel |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH10140292A (en) |
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012081510A (en) * | 2010-10-13 | 2012-04-26 | Sumitomo Metal Ind Ltd | Method for blooming high purity ferritic stainless 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 |
-
1996
- 1996-11-14 JP JP30261996A patent/JPH10140292A/en active Pending
Cited By (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2012081510A (en) * | 2010-10-13 | 2012-04-26 | Sumitomo Metal Ind Ltd | Method for blooming high purity ferritic stainless 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 |
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