JPH1190508A - Manufacture of austenitic stainless steel - Google Patents
Manufacture of austenitic stainless steelInfo
- Publication number
- JPH1190508A JPH1190508A JP25997997A JP25997997A JPH1190508A JP H1190508 A JPH1190508 A JP H1190508A JP 25997997 A JP25997997 A JP 25997997A JP 25997997 A JP25997997 A JP 25997997A JP H1190508 A JPH1190508 A JP H1190508A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- hot
- temp
- finish
- stainless steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、18％Cr−８％Ni
系などといったオーステナイト系ステンレス鋼板の製造
方法に関し、特に表面の美観が優れることが必要な建築
内外装品や浴槽、各種厨房器具などの使途に用いて好適
な、筋状模様の少ないオースナイト系ステンレス鋼板の
製造方法に関するものである。TECHNICAL FIELD The present invention relates to an 18% Cr-8% Ni
Austenitic stainless steel with less streak pattern suitable for use in interior and exterior products, bathtubs, various kitchen appliances, etc., which require particularly good surface aesthetics. The present invention relates to a method for manufacturing a steel sheet.
【０００２】[0002]
【従来の技術】オーステナイト系ステンレス鋼は、加工
性及び耐リジング性に優れていることから、建築内外装
品や浴槽、各種厨房器具などの分野で幅広く使用されて
いる。しかし、オーステナイト系ステンレス鋼は、鋼板
表面に縞状模様、すなわち光沢むらが発生することがあ
り、美観を著しく損ね、製品価値を低下させることか
ら、この筋状模様を軽減することが重要な課題となって
いる。このため、従来より光沢むらの発生を防止し、安
定した光沢を有するオーステナイト系ステンレス鋼板の
製造方法が提案され、公開された技術も少なくない。2. Description of the Related Art Austenitic stainless steel is widely used in the fields of building interior and exterior parts, bathtubs, various kitchen appliances, etc. because of its excellent workability and ridging resistance. However, in austenitic stainless steel, a striped pattern, that is, uneven gloss may occur on the surface of the steel sheet, which significantly impairs aesthetic appearance and lowers product value. It has become. For this reason, a method for producing an austenitic stainless steel sheet that prevents uneven gloss and has a stable gloss has been proposed, and there are many published techniques.
【０００３】例えば、特開昭６２−１７１３８号公報
は、オーステナイト系ステンレス鋼帯を連続焼鈍する前
に、特定の粘度の油を所定量だけ塗布する技術を開示し
ている。この技術は、鋼帯面に一様に酸化スケール層が
生成するようにして、圧延油や圧延摩耗粉の不均一付着
に由来した酸洗後の光沢むらを低減しようするものであ
る。また、特開平７−１５５８０９号公報は、冷延時に
使用するロールの表面粗度を順次粗いものから密にして
冷延する方法を提示している。これによれば、被圧延材
の前履歴の影響をあまり受けずに、高光沢でかつ均一な
光沢面を有するステンレス鋼板を得ることができるとさ
れている。For example, Japanese Patent Application Laid-Open No. Sho 62-17138 discloses a technique in which a predetermined amount of oil having a specific viscosity is applied before continuously annealing an austenitic stainless steel strip. This technique is intended to uniformly form an oxide scale layer on the surface of a steel strip to reduce unevenness in gloss after pickling caused by uneven adhesion of rolling oil and rolling wear powder. Japanese Patent Application Laid-Open No. Hei 7-155809 discloses a method in which the rolls used during cold rolling are sequentially cold-rolled from coarser to denser ones. According to this, it is said that a stainless steel sheet having a high gloss and a uniform gloss surface can be obtained without being largely affected by the previous history of the material to be rolled.
【０００４】[0004]
【発明が解決しようとする課題】しかしながら、上記特
開昭６２−１７１３８号公報、特開平７−１５５８０９
号公報に開示されたた技術は、いずれも設備改造を伴
い、製造コストが増加するという問題があった。However, the above-mentioned Japanese Patent Application Laid-Open No. Sho 62-17138 and Japanese Patent Application Laid-Open No.
Each of the techniques disclosed in the above-mentioned publications involves a problem that the equipment is remodeled and the manufacturing cost is increased.
【０００５】そこで、この発明の主たる目的は、上記既
知技術が抱えている、上述した設備改造の必要を懸念す
る必要のない、筋状模様の少ないオーステナイト系ステ
ンレス鋼板の製造方法を提案することにある。Therefore, a main object of the present invention is to propose a method of manufacturing an austenitic stainless steel sheet with few streak patterns, which does not need to be concerned with the above-mentioned equipment remodeling, which the above-mentioned known technology has. is there.
【０００６】[0006]
【課題を解決するための手段】さて、発明者らは、上記
課題の解決に向け、特に熱間圧延工程に着目して製造条
件を詳細に検討した結果、筋状模様は熱延中の再結晶挙
動の局所的な差異による表面光沢むらに起因することを
推定し、そして、実際に仕上げ圧延を適正に制御するこ
とによって、設備改造を伴うことなしに筋状模様の少な
いオーステナイト系ステンレス鋼板を製造することがで
き、この発明の目的を達成し得ることを知見した。この
発明は、この知見に基づき完成させたものであり、その
要旨は下記のとおりである。Means for Solving the Problems In order to solve the above-mentioned problems, the present inventors have studied the manufacturing conditions in detail with a particular focus on the hot rolling step. By estimating that it is caused by uneven surface gloss due to local differences in crystal behavior, and by appropriately controlling the finish rolling, it is possible to produce an austenitic stainless steel sheet with few streak patterns without equipment modification. It has been found that they can be manufactured and can achieve the object of the present invention. The present invention has been completed based on this finding, and the gist is as follows.
【０００７】オーステナイト系ステンレス鋼鋳片を、粗
圧延機及び仕上圧延機によって熱間圧延するにあたり、
仕上圧延終了温度ＦＤＴを、仕上圧延開始温度ＦＥＴよ
りも高くする圧延を行うことを特徴とするオーステナイ
ト系ステンレス鋼の製造方法。In hot rolling an austenitic stainless steel slab by a rough rolling mill and a finishing rolling mill,
A method for producing an austenitic stainless steel, wherein rolling is performed such that the finish rolling end temperature FDT is higher than the finish rolling start temperature FET.
【０００８】[0008]
【発明の実施の形態】以下、この発明を、実験結果に基
づいてより具体的に説明する。SUS 304 （0.05wt％Ｃ−
0.50wt％Si−1.05％Mn−0.033 wt％Ｐ−0.02Ｓwt％Al−
0.040 wt％Ｎ−18.2wt％Cr−8.4 wt％Ni）及びSUS 316
（0.06％Ｃ−0.60wt％Si−1.02wt％Mn−0.035 wt％Ｐ−
0.02Ｓ−0.024 wt％Ｎ−16.9wt％Cr−10.6wt％Ni−2.2
wt％Mo−0.020 wt％Ti）の成分組成になる２種のステン
レス鋼スラブ（スラブ厚200 mm）を1260℃に加熱後、３
スタンドからなる圧延機を用いた粗圧延により30mm厚の
シートバーとした。次いで、このシートバーを７スタン
ドからなる圧延機による熱間仕上圧延により厚み5.0 mm
及び1.3 mmの２種類の熱延板に仕上げ、650 ℃で巻取っ
た。その後、5.0 mm厚の熱延板は熱延板焼鈍、酸洗を経
て、厚み0.4 mmまで冷間圧延した後、仕上焼鈍した。ま
た、1.4 mm厚の熱延板は、熱延板焼鈍のままで試験に供
した。なお、熱延板焼鈍はSUS 304 については1150℃、
SUS 316 は1160℃で行った。仕上焼鈍温度は、SUS 304
は1120℃とし、SUS316 は1135℃とした。BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described more specifically based on experimental results. SUS 304 (0.05wt% C-
0.50wt% Si-1.05% Mn-0.033wt% P-0.02Swt% Al-
0.040 wt% N-18.2 wt% Cr-8.4 wt% Ni) and SUS316
(0.06% C-0.60wt% Si-1.02wt% Mn-0.035wt% P-
0.02S-0.024wt% N-16.9wt% Cr-10.6wt% Ni-2.2
After heating two kinds of stainless steel slabs (slab thickness 200 mm) having the composition of wt% Mo-0.020 wt% Ti) to 1260 ° C,
A sheet bar having a thickness of 30 mm was obtained by rough rolling using a rolling mill including a stand. Next, this sheet bar was subjected to hot finish rolling by a rolling mill comprising seven stands to a thickness of 5.0 mm.
And 1.3 mm, and rolled at 650 ° C. Thereafter, the hot-rolled sheet having a thickness of 5.0 mm was subjected to hot-rolled sheet annealing, pickling, cold-rolled to a thickness of 0.4 mm, and then finish-annealed. In addition, the hot-rolled sheet having a thickness of 1.4 mm was subjected to the test while the hot-rolled sheet was annealed. The hot-rolled sheet was annealed at 1150 ° C for SUS 304,
SUS 316 was performed at 1160 ° C. Finish annealing temperature is SUS 304
Was 1120 ° C, and SUS316 was 1135 ° C.
【０００９】得られた鋼帯について、コイル全幅につい
て鋼板表面の筋状模様の発生度合いをＡ（良好）〜Ｄ
（劣る）まで指数づけした。この指数付けは、コイル全
幅について、光沢度計にて１mm間隔で光沢度を測定し、
互いに隣接する測定点間での光沢度差が全て４未満のも
のを表面筋状模様指数Ａ、６未満４以上のものが存在す
る場合を表面筋状模様指数Ｂ、８未満６以上のものが存
在する場合を表面筋状模様指数Ｃ、８以上のものが存在
する場合を表面筋状模様指数Ｄとした。その結果を図１
に示す。同図(a) がSUS 304 、同図(b) がSUS 316 であ
る。In the obtained steel strip, the degree of occurrence of streak patterns on the surface of the steel sheet for the entire width of the coil is A (good) to D.
Indexed to (poor). For this indexing, the gloss was measured at 1 mm intervals with a gloss meter for the entire width of the coil.
When the glossiness difference between the measurement points adjacent to each other is less than 4, the surface streak index A is less than 4, and when there is less than 4 or more, the surface streak index B is less than 8, and 6 or less. The surface streak pattern index C was defined as the case where the sample was present, and the surface streak pattern index D was defined as the case where the sample was 8 or more. Figure 1 shows the results.
Shown in FIG. 3A shows SUS 304, and FIG. 3B shows SUS 316.
【００１０】図１から、SUS 304 、SUS 316 いずれにお
いても、また、熱延板、冷延板いずれにおいても、熱間
仕上圧延終了温度（ＦＤＴ）が熱間圧延開始温度（ＦＥ
Ｔ）よりも高い場合に、筋状模様が大きく改善されてい
ることがわかる。以上の結果より、この発明において
は、熱間仕上圧延終了温度（ＦＤＴ）を熱間圧延開始温
度（ＦＥＴ）よりも高くすることを必須要件とする。な
お、ＦＥＴとＦＤＴに関しては、ともに900 〜1200℃の
範囲にあることが望ましい。FIG. 1 shows that the hot finish rolling end temperature (FDT) is the hot rolling start temperature (FE) in both SUS 304 and SUS 316, and in both hot-rolled and cold-rolled sheets.
It can be seen that when higher than T), the streak pattern is greatly improved. From the above results, in the present invention, it is an essential requirement that the hot finish rolling end temperature (FDT) be higher than the hot rolling start temperature (FET). It is desirable that both the FET and the FDT are in the range of 900 to 1200 ° C.
【００１１】この発明に従い、熱間仕上圧延終了温度
（ＦＤＴ）を熱間圧延開始温度（ＦＥＴ）よりも高くす
ることにより筋状模様が改善できた理由については明ら
かでないが、以下のように推察される。オーステナイト
系ステンレス鋼は、熱延中に再結晶が起こり、再結晶核
が加工後直ちに成長する過程が進行する。ここに、筋状
模様は熱延中の再結晶に局所的な差異を生じ、表面光沢
むらが生じることによると考えられ、そこでこの発明に
おいては、熱間仕上圧延終了温度（ＦＤＴ）を熱間圧延
開始温度（ＦＥＴ）よりも高くすることにより、再結晶
をパス間で促進させるものである。かくして、加工によ
る発熱を積極的に活用することにより均一な組織が実現
され、筋状模様を軽減できたものと推察される。According to the present invention, it is not clear why the streak pattern can be improved by setting the hot finish rolling end temperature (FDT) higher than the hot rolling start temperature (FET), but it is inferred as follows. Is done. Austenitic stainless steel undergoes recrystallization during hot rolling, and the process of growing recrystallization nuclei immediately after processing proceeds. Here, the streak pattern is considered to be caused by a local difference in recrystallization during hot rolling and uneven surface gloss. Therefore, in the present invention, the hot finish rolling end temperature (FDT) is set to By making the temperature higher than the rolling start temperature (FET), recrystallization is promoted between passes. Thus, it is presumed that a uniform structure was realized by actively utilizing the heat generated by the processing, and the streak pattern could be reduced.
【００１２】このように、熱間仕上圧延終了温度を熱間
圧延開始温度よりも高くする具体的手段としては、例え
ば、圧延速度を高めること、加工率を高くすること、ロ
ールクーラントの水量を調節することなどがある。な
お、より均一な組織を得るための手段としては、熱間仕
上圧延終了温度を熱間圧延開始温度よりも高くすること
に加えて、油潤滑圧延などを行うことも有効である。[0012] As described above, specific means for making the hot finish rolling end temperature higher than the hot rolling start temperature include, for example, increasing the rolling speed, increasing the working ratio, and adjusting the amount of water in the roll coolant. There are things to do. As a means for obtaining a more uniform structure, it is also effective to perform oil lubrication rolling in addition to making the hot finish rolling end temperature higher than the hot rolling start temperature.
【００１３】この発明が適用されるオーステナイト系ス
テンレス鋼は、その具体的組成としては、Cr量が15wt％
以上のオーステナイト系ステンレス鋼であれば、その種
を問わない。Cr以外の合金成分については、オーステナ
イト系ステンレス鋼に含有される範囲で、適宜含有させ
ることができる。次に、圧延素材の製造方法について
は、造塊−分塊圧延はもちろん、連続鋳造法により得ら
れる鋼片も適用できる。鋼片の加熱温度は、表面品質お
よび材料特性の観点から、1100〜1400℃の範囲が適当で
ある。加熱に引き続いて、熱間粗圧延を行い、次いで、
この発明に従い、熱間仕上圧延終了温度（ＦＤＴ）を熱
間圧延開始温度（ＦＥＴ）よりも高くする圧延を行う。The austenitic stainless steel to which the present invention is applied has a specific composition in which the Cr content is 15 wt%.
Any kind of austenitic stainless steel can be used. Alloy components other than Cr can be appropriately contained within the range contained in the austenitic stainless steel. Next, as a method for producing a rolled material, not only ingot-bulking rolling but also a steel slab obtained by a continuous casting method can be applied. The heating temperature of the steel slab is suitably in the range of 1100 to 1400 ° C. from the viewpoint of surface quality and material properties. Following the heating, hot rough rolling was performed, and then
According to the present invention, rolling is performed so that the hot finish rolling end temperature (FDT) is higher than the hot rolling start temperature (FET).
【００１４】以上説明したように、熱間圧延、特に熱間
仕上圧延をこの発明によって適正に制御し熱延鋼板とし
た後、熱延板焼鈍−冷延−仕上圧延焼鈍の工程を施す冷
延鋼板や冷延鋼帯は勿論のこと、熱延板焼鈍のままで冷
間圧延や仕上焼鈍を行わない工程による熱延鋼板、熱延
鋼帯としても、筋状模様の少ないオーステナイト系ステ
ンレス鋼板を製造することができる。As described above, after the hot rolling, particularly the hot finish rolling, is properly controlled according to the present invention to obtain a hot rolled steel sheet, the cold rolling is performed in the steps of hot rolled sheet annealing, cold rolling and finish rolling annealing. Austenitic stainless steel sheets with few streak patterns are used not only for steel sheets and cold-rolled steel strips, but also for hot-rolled steel sheets and hot-rolled steel strips that are not subjected to cold rolling or finish annealing while hot-rolled sheet annealing is performed. Can be manufactured.
【００１５】[0015]
【実施例】表１に示す化学組成になる連続鋳造スラブ
（厚み200 mm）を加熱後、３スタンドからなる粗圧延機
によりシートバーとし、このシートバーを、７スタンド
からなる仕上圧延機により、種々の条件で熱間仕上圧延
を施して熱延板に仕上げた。このとき、仕上げ圧延機全
スタンドでの平均歪速度を変えて、仕上圧延終了温度
（ＦＤＴ）及び仕上圧延開始温度（ＦＥＴ）を制御した
が、具体的な値は鋼種と板厚によって異なる。更に、こ
の熱延板に酸洗を施したのち、冷間圧延、仕上焼鈍し鋼
帯を製造した。また、一部の試料については、上記工程
のうち、冷間圧延及び仕上圧延を省略した工程による鋼
帯も製造した。これらの鋼帯の製造条件を表２〜４に示
す。EXAMPLE A continuous cast slab (thickness: 200 mm) having the chemical composition shown in Table 1 was heated and then converted into a sheet bar by a three-stand rough rolling mill. The sheet bar was converted by a seven-stand finishing mill. Hot finish rolling was performed under various conditions to finish a hot rolled sheet. At this time, the finish rolling end temperature (FDT) and the finish rolling start temperature (FET) were controlled by changing the average strain rate in all stands of the finishing mill, but specific values differ depending on the steel type and the sheet thickness. Further, after pickling this hot-rolled sheet, cold rolling and finish annealing were performed to produce a steel strip. Further, for some of the samples, a steel strip was also manufactured by a process in which the cold rolling and the finish rolling were omitted from the above processes. Tables 2 to 4 show the manufacturing conditions of these steel strips.
【００１６】[0016]
【表１】 [Table 1]
【００１７】[0017]
【表２】 [Table 2]
【００１８】[0018]
【表３】 [Table 3]
【００１９】[0019]
【表４】 [Table 4]
【００２０】得られた各鋼帯の先端から７m の位置にお
ける試験片を採取し、筋状模様を評価した。具体的に
は、表２に示した表面筋状模様評価は、得られた鋼帯に
ついて、圧延方向に300 mm長さの鋼板を採取し鋼板の全
幅にわたって筋状模様の発生度合いを指数付けしたもの
である。この指数付けは、コイル全幅について、光沢度
計にて１mm間隔で光沢度を測定し、互いに隣接する測定
点間での光沢度差が全て４未満のものを表面筋状模様指
数Ａ、６未満４以上のものが存在する場合を表面筋状模
様指数Ｂ、８未満６以上のものが存在する場合を表面筋
状模様指数Ｃ、８以上のものが存在する場合を表面筋状
模様指数Ｄとした。その結果を併せて表２に示す。この
発明に従う発明鋼は、熱延を経た後の工程によらず、い
ずれも筋状模様が大きく改善されていることがわかる。A test piece at a position 7 m from the tip of each of the obtained steel strips was sampled, and the streak pattern was evaluated. Specifically, in the evaluation of the surface streak pattern shown in Table 2, for the obtained steel strip, a steel sheet having a length of 300 mm in the rolling direction was sampled, and the degree of occurrence of the streak pattern was indexed over the entire width of the steel sheet. Things. For this indexing, the gloss was measured at 1 mm intervals with a gloss meter over the entire width of the coil, and the difference in gloss between adjacent measurement points was less than 4, and the surface streak pattern index A, less than 6 A surface streak pattern index B when 4 or more exist, a surface streak index C when less than 8 or more exist, and a surface streak index D when 8 or more exist. did. Table 2 also shows the results. It can be seen that the inventive steel according to the present invention has greatly improved streak patterns regardless of the process after hot rolling.
【００２１】[0021]
【発明の効果】以上、説明したように、この発明によれ
ば、筋状模様の少ないオーステナイト系ステンレス鋼板
を製造することが可能となる。また、この発明に関して
は、熱延板焼鈍に引き続き冷延−仕上焼鈍する工程、あ
るいは熱延板焼鈍を省略する工程によっても、熱延工程
以降の工程によらず、筋状模様の少ないステンレス鋼板
を製造する事ができるので、オーステナイト系ステンレ
ス鋼板の低コスト化に大きく寄与する。As described above, according to the present invention, it is possible to manufacture an austenitic stainless steel sheet having few streak patterns. In addition, according to the present invention, a stainless steel sheet having few streak patterns regardless of the steps after the hot rolling step, by the step of cold-rolling and finish annealing subsequent to the hot-rolled sheet annealing or the step of omitting the hot-rolled sheet annealing. , Which greatly contributes to cost reduction of austenitic stainless steel sheets.
【図１】仕上圧延終了温度ＦＤＴと仕上圧延開始温度Ｆ
ＥＴとの温度差が鋼板表面の筋状模様の発生状況に及ぼ
す影響を示す図である。FIG. 1 Finish rolling end temperature FDT and finish rolling start temperature F
It is a figure which shows the influence which the temperature difference with ET gives to the generation | occurrence | production state of the streak pattern on a steel plate surface.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 宇城 工 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 (72)発明者 佐藤 進 千葉県千葉市中央区川崎町１番地 川崎製 鉄株式会社技術研究所内 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Kouki Uki 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Inside the Technical Research Institute of Kawasaki Steel Co., Ltd. (72) Susumu Sato Susumu 1 Kawasaki-cho, Chuo-ku, Chiba City, Chiba Prefecture Kawasaki Steel Research Institute
Claims (1)
粗圧延機及び仕上圧延機によって熱間圧延するにあた
り、 仕上圧延終了温度ＦＤＴを、仕上圧延開始温度ＦＥＴよ
りも高くする圧延を行うことを特徴とするオーステナイ
ト系ステンレス鋼の製造方法。1. An austenitic stainless steel slab,
A method for producing austenitic stainless steel, comprising: performing hot rolling by a rough rolling mill and a finish rolling mill so that a finish rolling end temperature FDT is higher than a finish rolling start temperature FET.
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| JP25997997A JP3508500B2 (en) | 1997-09-25 | 1997-09-25 | Manufacturing method of austenitic stainless steel |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP25997997A JP3508500B2 (en) | 1997-09-25 | 1997-09-25 | Manufacturing method of austenitic stainless steel |
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| Publication Number | Publication Date |
|---|---|
| JPH1190508A true JPH1190508A (en) | 1999-04-06 |
| JP3508500B2 JP3508500B2 (en) | 2004-03-22 |
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|---|---|---|---|
| JP25997997A Expired - Fee Related JP3508500B2 (en) | 1997-09-25 | 1997-09-25 | Manufacturing method of austenitic stainless steel |
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Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016538422A (en) * | 2013-10-28 | 2016-12-08 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
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1997
- 1997-09-25 JP JP25997997A patent/JP3508500B2/en not_active Expired - Fee Related
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2016538422A (en) * | 2013-10-28 | 2016-12-08 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
| JP2019214076A (en) * | 2013-10-28 | 2019-12-19 | ザ・ナノスティール・カンパニー・インコーポレーテッド | Metal steel production by slab casting |
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|---|---|
| JP3508500B2 (en) | 2004-03-22 |
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