JPH08300124A - Production of austenitic stainless steel thin cast slab - Google Patents
Production of austenitic stainless steel thin cast slabInfo
- Publication number
- JPH08300124A JPH08300124A JP10387795A JP10387795A JPH08300124A JP H08300124 A JPH08300124 A JP H08300124A JP 10387795 A JP10387795 A JP 10387795A JP 10387795 A JP10387795 A JP 10387795A JP H08300124 A JPH08300124 A JP H08300124A
- Authority
- JP
- Japan
- Prior art keywords
- casting
- slab
- stainless steel
- austenitic stainless
- time
- 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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Links
Landscapes
- Metal Rolling (AREA)
- Continuous Casting (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Strip Materials And Filament Materials (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、鋳片と鋳型内壁面間に
相対速度差の無い、いわゆる同期式連続鋳造プロセスに
よって製品厚さに近いサイズのオーステナイト系ステン
レス鋼薄板鋳片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 method for producing an austenitic stainless steel sheet slab having a size close to the product thickness by a so-called synchronous continuous casting process in which there is no relative speed difference between the slab and the inner wall surface of the mold. Regarding
【０００２】[0002]
【従来の技術】従来、連続鋳造法によりステンレス鋼薄
板を製造するには、鋳型を鋳造方向に振動させながら、
厚さ１００mm以上の鋳片に鋳造し、得られた鋳片の表面
手入れを行ない、加熱炉において１０００℃以上に加熱
した後、ホットストリップミルによって熱間圧延を施
し、厚さ数mmのホットストリップとしていた。2. Description of the Related Art Conventionally, in order to manufacture a stainless steel thin plate by a continuous casting method, while vibrating a mold in a casting direction,
Hot strip with a thickness of several mm is cast into a slab with a thickness of 100 mm or more, the surface of the slab is cared for, heated to 1000 ° C or higher in a heating furnace, and hot-rolled with a hot strip mill. I was trying.
【０００３】従来のプロセスにおいては、長大な熱間圧
延設備で、材料の加熱及び加工を行うために多大のエネ
ルギーを必要とし、生産性の面でも優れた製造プロセス
とは言い難かった。長大な熱間圧延設備と多大なエネル
ギー、圧延動力を必要とするという問題を解決すべく、
近年、連続鋳造工程でホットストリップと同等か、或は
それに近い厚さの鋳片（薄帯）を得るプロセスの研究が
進められている。例えば、「鉄と鋼」 '８５，Ａ１９７
〜 'Ａ２５６において特集された論文に、ホットストリ
ップを連続鋳造によって直接的に得るプロセスが開示さ
れている。In the conventional process, a large amount of energy is required to heat and process the material in a long hot rolling facility, and it is difficult to say that the manufacturing process is excellent in productivity. In order to solve the problem of requiring long hot rolling equipment, enormous energy, rolling power,
In recent years, research on a process for obtaining a slab (thin band) having a thickness equal to or close to that of a hot strip in a continuous casting process has been advanced. For example, "Iron and Steel"'85, A197.
~ The paper featured in 'A256 discloses a process for directly obtaining hot strip by continuous casting.
【０００４】この種の方式の連続鋳造プロセスにおいて
は、最終製品形状に近い鋳片を製造し、熱延工程、熱処
理工程等の中間段階を省略又は簡略しているため、鋳片
の組織および表面性状等が製品の材質や表面性状に大き
な影響を与える。例えば、特開平２−１９４２６号公報
に述べられているように、冷間圧延後に鋳片の粗大な結
晶粒に起因するローピングと称される表面欠陥が発生す
ることが知られている。このようなローピングの対策と
して、特開平２−１９４２６号公報では鋳造後の冷却速
度の増大による結晶粒の成長抑制および２回冷延を施す
方法が提案されている。しかしながら、上記の発明では
熱間圧延を省略する代わりに冷間圧延・焼鈍工程を１回
追加する必要があるため、望ましい方法とは言えなかっ
た。In the continuous casting process of this type, since the cast product having a shape close to that of the final product is manufactured and intermediate steps such as the hot rolling process and the heat treatment process are omitted or simplified, the structure and surface of the cast product are obtained. Properties and the like have a great influence on the material and surface properties of the product. For example, as described in JP-A-2-19426, it is known that after cold rolling, surface defects called roping due to coarse crystal grains of a slab occur. As a countermeasure against such roping, Japanese Patent Application Laid-Open No. 2-19426 proposes a method of suppressing the growth of crystal grains by increasing the cooling rate after casting and performing cold rolling twice. However, in the above invention, it is necessary to add the cold rolling / annealing process once instead of omitting the hot rolling, and thus it cannot be said to be a desirable method.
【０００５】[0005]
【発明が解決しようとする課題】本発明は、かかる連続
鋳造プロセス、すなわち溶鋼から直接に板厚１０mm以下
の薄板鋳片を連続鋳造し、この薄板鋳片を冷間加工し
て、板厚０．５〜３mmのオーステナイト系ステンレス鋼
板を製造する方法において、前記薄板鋳片のγ粒を細粒
化することにより、製品のローピングを著しく低減でき
る表面品質の優れたオーステナイト系ステンレス鋼薄板
鋳片の製造方法を提供することを目的とする。SUMMARY OF THE INVENTION The present invention is directed to such a continuous casting process, that is, continuous casting of a thin sheet slab having a sheet thickness of 10 mm or less directly from molten steel, and cold working the thin sheet slab to obtain a sheet thickness of 0. In the method for producing an austenitic stainless steel sheet having a thickness of 0.5 to 3 mm, the roping of the thin plate slab is made finer to significantly reduce the roping of the product. It is intended to provide a manufacturing method.
【０００６】[0006]
【課題を解決するための手段】本発明は、オーステナイ
ト系ステンレス鋼薄板鋳片の鋳造において、鋳造前の溶
鋼成分を（１）式で定義されるδ−Ｆｅの値が７．５以
上となるように調整し、かつ（２）式で定義される鋳造
時の過熱度ΔＴを４０℃以下に調整し、さらに凝固時の
平均冷却速度を１００℃／sec 以上として鋳造すること
を特徴とするオーステナイト系ステンレス鋼薄板鋳片の
製造方法である。According to the present invention, in the casting of an austenitic stainless steel sheet slab, the value of δ-Fe defined by the formula (1) for the molten steel component before casting is 7.5 or more. And the superheat ΔT at the time of casting defined by the formula (2) is adjusted to 40 ° C. or less, and the average cooling rate at the time of solidification is 100 ° C./sec or more. It is a method of manufacturing a stainless steel thin plate cast slab.
【０００７】 δ−Ｆｅ＝３．０（Ｃｒ＋１．５Ｓｉ＋Ｍｏ） −２．８（Ｎｉ＋０．５Ｍｎ＋０．５Ｃｕ） −８４（Ｃ＋Ｎ）−１９．８ ……………………………（１） （各成分は重量％） ΔＴ ＝鋳造温度Ｔｃ（℃）−凝固開始温度Ｔｌ（℃）…………（２） Ｄａｖｅ＝Σ２×（３×Ｓｉ／２π）1/2 ×Ｓｉ／Ｓ …………（３） Ｓｉ；ｉ番目の粒の面積（μm2） Ｓ ；粒径の測定総面積（μm2） また、上記の鋳造に続いて、９００〜１２００℃の範囲
で圧下率が２０％以上の圧延を行い、引き続いて９００
〜１１５０℃の温度で熱処理することを特徴とするオー
ステナイト系ステンレス鋼薄板鋳片の製造方法である。Δ-Fe = 3.0 (Cr + 1.5Si + Mo) -2.8 (Ni + 0.5Mn + 0.5Cu) -84 (C + N) -19.8 ……………………………… (1) ( Each component is in weight%) ΔT = casting temperature Tc (° C.)-Solidification start temperature Tl (° C.) (2) Dave = Σ2 × (3 × Si / 2π) 1/2 × Si / S ... (3) Si; area of i-th grain (μm 2 ) S; total area of grain size measurement (μm 2 ). Further, following the above casting, a reduction rate of 20% or more in the range of 900 to 1200 ° C. Rolling, and then 900
A method for producing an austenitic stainless steel thin plate slab, characterized in that the heat treatment is performed at a temperature of ˜1150 ° C.
【０００８】[0008]
【作用】本発明者らは、双ロール（ツインドラム）式連
続鋳造などの急冷凝固組織は不均一な混粒組織であり、
従来用いられてきた結晶粒の個数頻度に対する期待値と
して定義されるＸ（＝Σ２×（３×Ｓｉ／２π）1/2 ／
Ｎ）では急冷凝固の混粒組織を代表できないことがわか
り、結晶粒の面積率に対する期待値として（３）式で定
義されるＤａｖｅを新たに定義した。The present inventors have found that the rapidly solidified structure such as twin roll (twin drum) continuous casting is a non-uniform mixed grain structure,
X (= Σ2 × (3 × Si / 2π) 1/2 / which is defined as an expected value for the frequency of the number of crystal grains that has been used conventionally
It was found that N) cannot represent the mixed grain structure of rapid solidification, and Dave defined by the equation (3) was newly defined as an expected value for the area ratio of crystal grains.
【０００９】本発明においては、δ−Ｆｅを７．５以上
にした場合には、凝固がδフェライト相を初晶として起
こり、固相でδ→γの変態が起こることになる。この場
合には微細なフェライトを分散していることにより、δ
→γの変態サイトの増加、またδフェライトによるγ粒
の成長のピニング効果によって、γ粒が微細化する。つ
まり、粗大な柱状晶を変態により分断化させることによ
り細粒化できると考えられる。In the present invention, when δ-Fe is 7.5 or more, solidification occurs with the δ ferrite phase as the primary crystal, and the δ → γ transformation occurs in the solid phase. In this case, since fine ferrite is dispersed, δ
→ The γ grains are refined due to the increase of γ transformation sites and the pinning effect of γ grain growth by δ ferrite. In other words, it is considered that coarse columnar crystals can be finely divided by dividing them by transformation.
【００１０】また、鋳造時の過熱度（ΔＴ）を低くして
鋳造することは粗大な柱状晶から幅の狭い、比較的微細
な柱状晶に変えることができることがわかった。このこ
とは、ΔＴが低い場合には凝固界面近傍の温度勾配が小
さく、結晶の成長が遅いために放出した潜熱が拡散しや
すく、周囲の結晶の成長を妨げることなく（ある特定結
晶が優先的に成長することなく）、微細な柱状晶が成長
していくためと考えられる。It has also been found that by casting with a low degree of superheat (ΔT) during casting, it is possible to change from coarse columnar crystals to narrow fine columnar crystals. This means that when ΔT is low, the temperature gradient in the vicinity of the solidification interface is small and the growth of crystals is slow, so the released latent heat is likely to diffuse, and the growth of surrounding crystals is not hindered (a certain specific crystal is preferentially). It is considered that fine columnar crystals grow without growing.
【００１１】また、凝固時の平均冷却速度を増大するこ
とにより、凝固ミクロ組織が微細化し、特に凝固時に初
晶として生成するδフェライトが微細に分散する。その
ために、δ→γの変態サイトの増加、またδフェライト
によるγ粒の成長のピニング効果が一層促進され、γ粒
が微細化すると考えられる。なお、凝固時の平均冷却速
度は冷却ロールの材質およびロール表面性状、凹凸によ
りコントロールできる。Further, by increasing the average cooling rate during solidification, the solidification microstructure becomes finer, and in particular, δ-ferrite produced as a primary crystal during solidification is finely dispersed. Therefore, it is considered that the increase of δ → γ transformation sites and the pinning effect of γ grain growth by δ ferrite are further promoted, and the γ grains are refined. The average cooling rate during solidification can be controlled by the material of the cooling roll, the surface properties of the roll, and the unevenness.
【００１２】本発明では、ΔＴおよび凝固時の平均冷却
速度の制御による凝固組織微細化と、δ−Ｆｅを制御す
ることによる変態微細化を組合わせることにより鋳片の
γ粒を微細化できるものである。さらに、本発明におけ
る鋳造に引き続いた圧延・熱処理は再結晶を利用した等
軸・細粒化組織を得る手法である。In the present invention, the γ grains of the cast slab can be refined by combining the refinement of the solidification structure by controlling ΔT and the average cooling rate during solidification and the refinement of the transformation by controlling δ-Fe. Is. Further, the rolling and heat treatment subsequent to the casting in the present invention is a method for obtaining an equiaxed grain refinement structure utilizing recrystallization.
【００１３】以下に本発明の内容について詳細に説明す
る。図１は本発明を実施する一手段としての双ロール
（ツインドラム）式連続鋳造装置１の概略側断面を示し
ている。所定幅の間隙を隔てて対向位置される一対の冷
却ロール２及び３の両端面に対しては、扇状のサイド堰
４が圧着されている。鋳造時、各冷却ロール２，３は駆
動機構によって図中、矢印に示すように互いに反対方向
に回転駆動され、冷却ロール２，３の外周面２ａ及び３
ａと両サイド堰４によって画成される湯溜り部５に対し
て、その上方に位置する注湯装置（図示せず）から、例
えばＳＵＳ３０４に代表されるようなオーステナイト系
ステンレス鋼の溶鋼６が供給される。The contents of the present invention will be described in detail below. FIG. 1 shows a schematic side section of a twin roll type continuous casting apparatus 1 as one means for carrying out the present invention. A fan-shaped side dam 4 is pressure-bonded to both end faces of a pair of cooling rolls 2 and 3 which are opposed to each other with a gap of a predetermined width. At the time of casting, the cooling rolls 2 and 3 are rotationally driven in opposite directions as indicated by arrows in the drawing by the drive mechanism, and the outer peripheral surfaces 2a and 3 of the cooling rolls 2 and 3 are rotated.
a molten metal 6 of austenitic stainless steel represented by SUS304, for example, from a pouring device (not shown) located above the molten metal pool 5 defined by a and both side dams 4. Supplied.
【００１４】そして溶鋼６は、冷却ロール２，３の外周
面２ａ，３ａと接触することにより抜熱され、湯面と外
周面２ａ，３ａとの接点近傍（メニスカスと呼ぶ）８に
生成した凝固シェル７ａ，７ｂは、ロールの回転に沿っ
て成長し、キッシングポイント９において互いに圧着さ
れる。このようにして連続してオーステナイト系ステン
レス鋼の薄板鋳片７が製造されることになる。The molten steel 6 is deheated by coming into contact with the outer peripheral surfaces 2a, 3a of the cooling rolls 2, 3 and solidified in the vicinity of the contact point (called meniscus) 8 between the molten metal surface and the outer peripheral surfaces 2a, 3a. The shells 7a, 7b grow along the rotation of the roll and are pressed together at the kissing point 9. In this way, the thin cast piece 7 of austenitic stainless steel is continuously manufactured.
【００１５】種々の組成のオーステナイト系ステンレス
鋼溶鋼を、前述の双ロール式連続鋳造機によって種々の
鋳造条件で、厚さ３mmの薄板鋳片に鋳造した。得られた
鋳片を酸洗した後、鋳片のＬ断面でγ粒径を観察し、
（３）式により平均粒径Ｄａｖｅを測定した。 Ｄａｖｅ＝Σ２×（３×Ｓｉ／２π）1/2 ×Ｓｉ／Ｓ …………（３） Ｓｉ；ｉ番目の粒の面積（μm2） Ｓ ；粒径の測定総面積（μm2） 図２に（１）式で計算されるδ−Ｆｅと鋳片の平均粒径
Ｄａｖｅの関係を示す。なお、ここで、（２）式で定義
される溶鋼過熱度ΔＴは４０℃以下、凝固時の平均冷却
速度は１００〜３００℃／sec とした。δ−Ｆｅを７．
５以上とすることにより、鋳片の平均粒径Ｄａｖｅが大
幅に低減できることがわかった。Austenitic stainless steel molten steels having various compositions were cast into thin plate cast pieces having a thickness of 3 mm under various casting conditions by the twin roll type continuous casting machine described above. After pickling the obtained slab, γ grain size is observed in the L cross section of the slab,
The average particle size Dave was measured by the formula (3). Dave = Σ2 × (3 × Si / 2π) 1/2 × Si / S (3) Si; area of i-th grain (μm 2 ) S; total area of grain size measurement (μm 2 ) 2 shows the relationship between δ-Fe calculated by the equation (1) and the average particle diameter Dave of the cast slab. Here, the molten steel superheat degree ΔT defined by the equation (2) was 40 ° C. or less, and the average cooling rate during solidification was 100 to 300 ° C./sec. δ-Fe is 7.
It was found that the average particle size Dave of the cast slab can be significantly reduced by setting it to 5 or more.
【００１６】図３に（２）式で計算されるΔＴと鋳片の
平均粒径Ｄａｖｅの関係を示す。ここで、鋳造温度Ｔｃ
は図１の双ロール間の溶鋼６の表面付近で測定した。ま
た、δ−Ｆｅは７．５以上、凝固時の平均冷却速度は１
００℃／sec 以上とした。ΔＴを４０℃以下とすること
により、鋳片の平均粒径Ｄａｖｅが大幅に低減できるこ
とがわかる。なお、溶鋼過熱度ΔＴは鋳造時の溶鋼の皮
張りの発生を考慮すると１０℃以上にすることが望まし
い。FIG. 3 shows the relationship between ΔT calculated by the equation (2) and the average particle diameter Dave of the slab. Where casting temperature Tc
Was measured near the surface of the molten steel 6 between the twin rolls in FIG. Further, δ-Fe is 7.5 or more, and the average cooling rate during solidification is 1
It was set to 00 ° C./sec or more. It can be seen that the average particle diameter Dave of the cast slab can be significantly reduced by setting ΔT to 40 ° C. or less. The molten steel superheat degree ΔT is preferably 10 ° C. or higher in consideration of the occurrence of skinning of the molten steel during casting.
【００１７】図４に凝固時の平均冷却速度と鋳片の平均
粒径Ｄａｖｅの関係を示す。ここで、凝固時の平均冷却
速度は鋳造温度Ｔｃと冷却ロール直下での鋳片温度の差
を鋳造速度より求められる経過時間で割ることにより算
出した。また、δ−Ｆｅは７．５以上、ΔＴは４０℃以
下とした。凝固時の平均冷却速度を１００℃／sec 以上
とすることにより、鋳片の平均粒径Ｄａｖｅが大幅に低
減できることがわかった。FIG. 4 shows the relationship between the average cooling rate during solidification and the average particle size Dave of the slab. Here, the average cooling rate during solidification was calculated by dividing the difference between the casting temperature Tc and the slab temperature immediately below the cooling roll by the elapsed time obtained from the casting rate. Further, δ-Fe was 7.5 or more and ΔT was 40 ° C or less. It was found that by setting the average cooling rate during solidification to 100 ° C./sec or more, the average particle diameter Dave of the slab can be significantly reduced.
【００１８】次に、本発明における圧延、熱処理条件に
ついて説明する。圧延温度は９００℃未満では鋼材の変
形抵抗が大きくなり、熱間圧延の負荷が大きいこと、お
よび形状制御が困難なことから不適当である。また、１
２００℃超では加工歪が開放されやすく、圧延による加
工歪付与の効果が小さくなること、および鋳片の加熱が
必要になるために経済的でないことから不適当である。
従って、圧延温度は９００〜１２００℃の範囲が適当で
ある。Next, the rolling and heat treatment conditions in the present invention will be described. If the rolling temperature is lower than 900 ° C., the deformation resistance of the steel material becomes large, the load of hot rolling is large, and it is difficult to control the shape. Also, 1
If it exceeds 200 ° C, the processing strain is likely to be released, the effect of imparting the processing strain by rolling becomes small, and it is not economical because heating of the slab is required, which is not suitable.
Therefore, the rolling temperature is appropriately in the range of 900 to 1200 ° C.
【００１９】圧下率は２０％未満では再結晶に必要な歪
量が得られないために、十分な組織微細化効果が得られ
ず、不適当である。従って圧下率を２０％以上とした。
熱処理温度は９００℃未満ではオーステナイト系ステン
レス鋼の再結晶が起こらないために不適当である。ま
た、再結晶を促進するためには高温が望ましいが、１１
５０℃超では加熱が必要になるために経済的でないこと
から不適当である。従って熱処理温度は９００〜１１５
０℃の範囲が適当である。なお、熱処理時間は熱処理温
度に依存するが、１１００℃では５sec 以上の熱処理時
間で再結晶できる。If the rolling reduction is less than 20%, the amount of strain required for recrystallization cannot be obtained, so that a sufficient effect of refining the structure cannot be obtained, which is unsuitable. Therefore, the rolling reduction is set to 20% or more.
If the heat treatment temperature is lower than 900 ° C., recrystallization of austenitic stainless steel does not occur, which is unsuitable. High temperature is desirable to promote recrystallization, but 11
If it exceeds 50 ° C, it is not economical because it requires heating and is not suitable. Therefore, the heat treatment temperature is 900 to 115
A range of 0 ° C is suitable. Although the heat treatment time depends on the heat treatment temperature, recrystallization can be performed at 1100 ° C. in a heat treatment time of 5 seconds or more.
【００２０】[0020]
【実施例】表１に示す種々の組成のオーステナイト系ス
テンレス鋼溶鋼を、双ロール式連続鋳造機によって、種
々の鋳造条件で（すなわちΔＴおよび凝固時の平均冷却
速度）、厚さ２〜４mmの薄帯状鋳片に鋳造し、凝固後は
１４００〜１２００℃までの温度域を１０〜３０℃／se
c の冷却温度で冷却し、その後引き続き空冷で室温まで
冷却した。得られた鋳片の結晶粒径を測定した。また、
表２は表１と同様に種々の組成のオーステナイト系ステ
ンレス鋼溶鋼を、双ロール式連続鋳造機によって、種々
の鋳造条件で（すなわちΔＴおよび凝固時の平均冷却速
度）、厚さ２〜４mmの薄帯状鋳片に鋳造し、引き続い
て、圧延・熱処理を行った。得られた鋳片は酸洗した
後、５０％から８５％の圧下率でそれぞれ冷間圧延し、
その後最終焼鈍、酸洗、および調質圧延した。得られた
薄板製品のローピングを評価した。なお、ローピング高
さは許容範囲内（０．２μｍ以下）のものを良好、許容
範囲外のものを不良とした。EXAMPLES Molten austenitic stainless steels having various compositions shown in Table 1 were produced by a twin roll type continuous casting machine under various casting conditions (that is, ΔT and average cooling rate during solidification) with a thickness of 2 to 4 mm. Cast into thin strip slabs, and after solidification, the temperature range from 1400 to 1200 ° C is 10 to 30 ° C / se
It was cooled at the cooling temperature of c and then cooled by air cooling to room temperature. The crystal grain size of the obtained cast piece was measured. Also,
Similar to Table 1, Table 2 shows austenitic stainless steel molten steel having various compositions under a variety of casting conditions (that is, ΔT and an average cooling rate during solidification) by a twin roll type continuous casting machine and having a thickness of 2 to 4 mm. The strip was cast into a strip and subsequently rolled and heat-treated. The obtained slabs were pickled and then cold-rolled at a reduction rate of 50% to 85%,
After that, final annealing, pickling, and temper rolling were performed. The roping of the obtained thin plate product was evaluated. The roping height within the permissible range (0.2 μm or less) was evaluated as good, and the one outside the permissible range was evaluated as poor.
【００２１】[0021]
【表１】 [Table 1]
【００２２】[0022]
【表２】 [Table 2]
【００２３】上記結果から、本発明に従って、δ−Ｆ
ｅ，ΔＴ，凝固時の平均冷却速度を適正にした場合は、
γ粒径が細粒化されることがわかる。また、鋳造に引き
続いて、圧延・熱処理を行った。この場合における本発
明例では、ローピング高さは許容範囲内（０．２μｍ以
下）であるのに対し、本発明の範囲から外れた条件をも
つ比較例ではローピング高さが許容範囲を越え、製品の
表面品質は不良であった。From the above results, according to the present invention, δ-F
If e, ΔT, and the average cooling rate during solidification are set appropriately,
It can be seen that the γ grain size is reduced. After casting, rolling and heat treatment were performed. In the case of the present invention in this case, the roping height is within the allowable range (0.2 μm or less), whereas in the comparative example having a condition outside the range of the present invention, the roping height exceeds the allowable range and the product Had a poor surface quality.
【００２４】[0024]
【発明の効果】以上説明したように、本発明によれば、
オーステナイト系ステンレス鋼の薄板鋳片製造におい
て、鋳片組織を微細化することにより製品薄板のローピ
ングを防止することができる。As described above, according to the present invention,
In the production of an austenitic stainless steel sheet slab, by refining the slab structure, roping of the product sheet can be prevented.
【図１】双ロール式連続鋳造装置の概略側断面である。FIG. 1 is a schematic side section of a twin roll type continuous casting apparatus.
【図２】溶鋼のδ−Ｆｅ（％）と鋳片の平均粒径（μ
ｍ）との関係を示す図である。[Fig. 2] δ-Fe (%) of molten steel and average particle size (μ
It is a figure which shows the relationship with m).
【図３】鋳造時の過熱温度ΔＴ（℃）と鋳片の平均粒径
（μｍ）との関係を示す図である。FIG. 3 is a diagram showing a relationship between a superheating temperature ΔT (° C.) during casting and an average particle diameter (μm) of a slab.
【図４】凝固時の平均冷却速度（℃／sec ）と鋳片の平
均粒径（μｍ）との関係を示す図である。FIG. 4 is a diagram showing the relationship between the average cooling rate (° C./sec) during solidification and the average particle size (μm) of the slab.
１…双ロール式連続鋳造装置 ２，３…冷却ロール ４…両サイド堰 ５…湯溜り部 ６…溶鋼 ７…薄板鋳片 1 ... Twin roll type continuous casting device 2, 3 ... Cooling roll 4 ... Both side dams 5 ... Hot water pool part 6 ... Molten steel 7 ... Thin plate slab
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｂ２２Ｄ 11/16 Ｂ２２Ｄ 11/16 Ｚ Ｃ２１Ｄ 6/00 １０２ Ｃ２１Ｄ 6/00 １０２Ａ 8/02 9270−4Ｋ 8/02 Ｄ 9/52 １０１ 9/52 １０１ Ｃ２２Ｃ 38/00 ３０２ Ｃ２２Ｃ 38/00 ３０２Ｚ 38/44 38/44 (72)発明者 上島 良之 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 the front page (51) Int.Cl. 6 Identification code Office reference number FI Technical display location B22D 11/16 B22D 11/16 Z C21D 6/00 102 C21D 6/00 102A 8/02 9270-4K 8/02 D 9/52 101 9/52 101 C22C 38/00 302 C22C 38/00 302Z 38/44 38/44 (72) Inventor Yoshiyuki Uejima 20-1 Shintomi, Futtsu City, Chiba Nippon Steel Co., Ltd. Within the development headquarters
Claims (2)
の製造において、鋳造前の溶鋼成分を（１）式で定義さ
れるδ−Ｆｅの値が７．５以上となるように調整し、か
つ（２）式で定義される鋳造時の過熱度ΔＴを４０℃以
下に制御し、さらに凝固時の平均冷却速度を１００℃／
sec 以上として鋳造することを特徴とするオーステナイ
ト系ステンレス鋼薄板鋳片の製造方法。 δ−Ｆｅ＝３．０（Ｃｒ＋１．５Ｓｉ＋Ｍｏ） −２．８（Ｎｉ＋０．５Ｍｎ＋０．５Ｃｕ） −８４（Ｃ＋Ｎ）−１９．８ ……………………………（１） （各成分は重量％） ΔＴ ＝鋳造温度Ｔｃ（℃）−凝固開始温度Ｔｌ（℃）…………（２）1. In the production of an austenitic stainless steel sheet slab, the molten steel composition before casting is adjusted so that the value of δ-Fe defined by the formula (1) is 7.5 or more, and (2) The superheat ΔT at the time of casting defined by the formula) is controlled to 40 ° C or less, and the average cooling rate at the time of solidification is 100 ° C /
A method for producing an austenitic stainless steel sheet slab, characterized by casting as sec or more. δ-Fe = 3.0 (Cr + 1.5Si + Mo) -2.8 (Ni + 0.5Mn + 0.5Cu) -84 (C + N) -19.8 ………………………… (1) (Each component is %) ΔT = casting temperature Tc (° C.)-Solidification start temperature Tl (° C.) (2)
００〜１２００℃の範囲で圧下率が２０％以上の圧延を
行い、引き続いて９００〜１１５０℃の温度で熱処理す
ることを特徴とするオーステナイト系ステンレス鋼薄板
鋳片の製造方法。2. Following the casting of claim 1, 9
A method for producing an austenitic stainless steel thin sheet slab, which comprises rolling at a rolling reduction of 20% or more in a range of 00 to 1200 ° C, and subsequently heat treating at a temperature of 900 to 1150 ° C.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10387795A JP3423818B2 (en) | 1995-04-27 | 1995-04-27 | Method for producing austenitic stainless steel sheet slab |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10387795A JP3423818B2 (en) | 1995-04-27 | 1995-04-27 | Method for producing austenitic stainless steel sheet slab |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08300124A true JPH08300124A (en) | 1996-11-19 |
| JP3423818B2 JP3423818B2 (en) | 2003-07-07 |
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ID=14365675
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10387795A Expired - Fee Related JP3423818B2 (en) | 1995-04-27 | 1995-04-27 | Method for producing austenitic stainless steel sheet slab |
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| Country | Link |
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11181554A (en) * | 1997-12-22 | 1999-07-06 | Nippon Steel Corp | Chrome-nickel base stainless steel thin sheet excellent in surface quality and workability and its production |
| KR100450612B1 (en) * | 1999-08-19 | 2004-09-30 | 주식회사 포스코 | A continuous casting method of austenitic stainless steel containing high si content |
| KR100579389B1 (en) * | 2001-12-24 | 2006-05-12 | 주식회사 포스코 | continuous casting method of 310S austenite stainless steel |
| JP2012502186A (en) * | 2008-09-11 | 2012-01-26 | ティッセンクルップ ニロスタ ゲゼルシャフト ミット ベシュレンクテル ハフツング | Stainless steel, cold rolled strip made from this steel, and method for producing flat steel products from this steel |
| JP2015062948A (en) * | 2013-09-26 | 2015-04-09 | 新日鐵住金株式会社 | Scum weir and method and apparatus for production of thin slab |
| WO2018117480A1 (en) * | 2016-12-23 | 2018-06-28 | 주식회사 포스코 | Austenitic stainless steel processed product having excellent surface characteristics, and manufacturing method therefor |
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1995
- 1995-04-27 JP JP10387795A patent/JP3423818B2/en not_active Expired - Fee Related
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH11181554A (en) * | 1997-12-22 | 1999-07-06 | Nippon Steel Corp | Chrome-nickel base stainless steel thin sheet excellent in surface quality and workability and its production |
| KR100450612B1 (en) * | 1999-08-19 | 2004-09-30 | 주식회사 포스코 | A continuous casting method of austenitic stainless steel containing high si content |
| KR100579389B1 (en) * | 2001-12-24 | 2006-05-12 | 주식회사 포스코 | continuous casting method of 310S austenite stainless steel |
| JP2012502186A (en) * | 2008-09-11 | 2012-01-26 | ティッセンクルップ ニロスタ ゲゼルシャフト ミット ベシュレンクテル ハフツング | Stainless steel, cold rolled strip made from this steel, and method for producing flat steel products from this steel |
| JP2015062948A (en) * | 2013-09-26 | 2015-04-09 | 新日鐵住金株式会社 | Scum weir and method and apparatus for production of thin slab |
| WO2018117480A1 (en) * | 2016-12-23 | 2018-06-28 | 주식회사 포스코 | Austenitic stainless steel processed product having excellent surface characteristics, and manufacturing method therefor |
| KR20180073877A (en) * | 2016-12-23 | 2018-07-03 | 주식회사 포스코 | Austenitic stainless steel product having excellent surface properties and manufacturing method of the same |
| EP3561127A4 (en) * | 2016-12-23 | 2019-10-30 | Posco | Austenitic stainless steel having excellent processability and surface characteristics, and manufacturing method therefor |
| EP3561125A4 (en) * | 2016-12-23 | 2019-10-30 | Posco | Austenitic stainless steel processed product having excellent surface characteristics, and manufacturing method therefor |
| JP2020509210A (en) * | 2016-12-23 | 2020-03-26 | ポスコＰｏｓｃｏ | Austenitic stainless steel workpiece with excellent surface properties and method for producing the same |
| US11299799B2 (en) | 2016-12-23 | 2022-04-12 | Posco | Austenitic stainless steel product having excellent surface properties and manufacturing method of the same |
| US11542569B2 (en) | 2016-12-23 | 2023-01-03 | Posco Co., Ltd. | Austenitic stainless steel having excellent processability and surface characteristics, and manufacturing method therefor |
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|---|---|
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