JPH0261007A - Production of austenitic stainless steel foil - Google Patents
Production of austenitic stainless steel foilInfo
- Publication number
- JPH0261007A JPH0261007A JP21434488A JP21434488A JPH0261007A JP H0261007 A JPH0261007 A JP H0261007A JP 21434488 A JP21434488 A JP 21434488A JP 21434488 A JP21434488 A JP 21434488A JP H0261007 A JPH0261007 A JP H0261007A
- Authority
- JP
- Japan
- Prior art keywords
- foil
- stainless steel
- austenitic stainless
- cold rolling
- thin plate
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000963 austenitic stainless steel Inorganic materials 0.000 title claims abstract description 30
- 238000004519 manufacturing process Methods 0.000 title claims description 20
- 239000011888 foil Substances 0.000 title abstract 12
- 238000005097 cold rolling Methods 0.000 claims abstract description 26
- 239000013078 crystal Substances 0.000 claims abstract description 25
- 238000000137 annealing Methods 0.000 claims abstract description 14
- 238000001816 cooling Methods 0.000 claims description 4
- 238000000034 method Methods 0.000 abstract description 17
- 229910000831 Steel Inorganic materials 0.000 abstract description 14
- 239000010959 steel Substances 0.000 abstract description 14
- 238000007712 rapid solidification Methods 0.000 abstract description 4
- 238000010438 heat treatment Methods 0.000 abstract 3
- 229910001220 stainless steel Inorganic materials 0.000 description 9
- 239000010935 stainless steel Substances 0.000 description 7
- 238000005098 hot rolling Methods 0.000 description 5
- 229910000881 Cu alloy Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000010410 layer Substances 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 238000009749 continuous casting Methods 0.000 description 3
- 230000006911 nucleation Effects 0.000 description 3
- 238000010899 nucleation Methods 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 230000008023 solidification Effects 0.000 description 3
- 238000001000 micrograph Methods 0.000 description 2
- 230000008520 organization Effects 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 239000002344 surface layer Substances 0.000 description 2
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000015271 coagulation Effects 0.000 description 1
- 238000005345 coagulation Methods 0.000 description 1
- 239000004035 construction material Substances 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0405—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing of ferrous alloys
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
本発明はオーステナイト系ステンレス鋼薄板帯の製造方
法に関し、さらに詳しくは、異方性が小さく、かっ、良
好な機械的性質を有するオーステナイト系ステンレス鋼
薄板帯の製造方法に関するしのである。Detailed Description of the Invention [Industrial Application Field] The present invention relates to a method for manufacturing an austenitic stainless steel thin plate strip, and more particularly, to an austenitic stainless steel sheet having low anisotropy and good mechanical properties. This paper relates to a method for producing steel thin plate strips.
［従来技術］
一般に、ＳＵＳ ３０４で代表されるオーステナイト
系ステンレス鋼は、耐蝕性および成形加工性が良好であ
ることから、深絞り加工等により成形品として各種台所
用品、電気機器部品、建築用材料等に広く使用されてき
ている。[Prior art] Generally, austenitic stainless steel represented by SUS 304 has good corrosion resistance and formability, so it can be used as molded products by deep drawing etc. for various kitchen utensils, electrical equipment parts, and construction materials. It has been widely used.
従来、上記に説明したような各用途に使用されているオ
ーステナイト系ステンレス鋼板は、他の鋼板製造と同様
に連続鋳造法により製造された鋳片を、熱間圧延により
製造された後のコイルをさらに冷間圧延してから、焼鈍
を行なう工程により製造することが通常行なわれてきて
いる。Traditionally, austenitic stainless steel sheets used for various purposes as explained above are manufactured by using cast slabs manufactured by continuous casting as in other steel sheet manufacturing methods, and coils manufactured by hot rolling. It has been customary to manufacture the material through a process of further cold rolling and then annealing.
しかして、このような製造方法では何れにしても熱間圧
延や焼鈍により面内異方性や結晶粒粗大化が生成し易い
ため、例えば、特開昭６２−１９７２４７号公報に記載
されているように、ロールの回転表面上においてオース
テナイト系ステンレス溶鋼を連続的に急冷・凝固するこ
とにより、薄板帯を製造し、この薄板帯をそのまま冷間
圧延を行なうストリップキャスター法か提案されている
。However, in any of these manufacturing methods, in-plane anisotropy and crystal grain coarsening are likely to occur due to hot rolling and annealing. A strip caster method has been proposed, in which a thin plate strip is manufactured by continuously rapidly cooling and solidifying molten austenitic stainless steel on the rotating surface of a roll, and this thin plate strip is directly cold rolled.
しかしながら、この方法を行なおうとしても、薄板帯そ
のものは凝固組織を有しているので、これから製造され
たオーステナイト系ステンレス鋼板の機械的性質が従来
の方法による鋼板よりも劣るという問題があり、実用化
には至っていないのが現状である。However, even if this method is attempted, since the thin plate itself has a solidified structure, there is a problem that the mechanical properties of the austenitic stainless steel sheet manufactured from it are inferior to the steel sheet produced by the conventional method. At present, it has not been put into practical use.
［発明が解決しようとする課題］
本発明は上記に説明したように、従来の急冷・凝固薄板
帯の問題点を解消するために、本発明者か鋭意研究を行
ない、検討を重ねた結果、鋼板製造工程において大幅な
省力化とエネルギーの節減を図ることによって、従来法
により製造された鋼板と同等の良好な機械的性質を有す
るオーステナイト系ステンレス鋼薄板帯の製造方法を開
発したのである。[Problems to be Solved by the Invention] As explained above, the present invention has been developed as a result of intensive research and repeated consideration by the present inventor in order to solve the problems of the conventional rapidly quenched and solidified thin plate strip. By significantly reducing labor and energy in the steel sheet manufacturing process, we have developed a method for manufacturing austenitic stainless steel thin strips that have mechanical properties equivalent to those of conventionally manufactured steel sheets.
［課題を解決するための手段］
本発明に係るオーステナイト系ステンレス鋼薄板帯の製
造方法は、
（１）単ロール、双ロールの何れか１種のロールの回転
表面上において、オーステナイト系ステンレス鋼を連続
的に急冷・凝固することにより薄板帯を製造し、次いで
、この薄板帯の凝固組織が柱状晶で板厚に占める比率か
７５％以上の場合には、１０５０〜１１５０℃の温度に
おいて２〜１０分の溶体化処理を行ない、また、柱状晶
の板厚に占める比率が７５％以下であれば凝固状態のま
まか、或いは、重犯溶体化処理を行ない、その後、冷間
圧延率５０〜８０％の冷間圧延を行ない、さらに、１０
００〜１１５０℃の温度において０．５〜ＩＯ分の最終
焼鈍を行なうことを特徴とするオーステナイト系ステン
レス鋼薄板帯の製造方法を第１の発明とし、
（２）オーステナイト系ステンレス鋼薄板帯の厚さは５
＋ｎｍ以下であることを特徴とする特許請求の範囲第１
項記載のオーステナイト系ステンレス鋼薄板帯の製造方
法を第２の発明とする２つの発明よりなるものである。[Means for Solving the Problems] The method for producing an austenitic stainless steel thin plate strip according to the present invention includes: (1) austenitic stainless steel is coated on the rotating surface of either a single roll or a twin roll; A thin plate strip is manufactured by continuous rapid cooling and solidification, and then, if the solidified structure of this thin plate strip is columnar crystals that account for 75% or more of the plate thickness, the thin plate strip is heated at a temperature of 1050 to 1150°C for 2 to 30 minutes. Solution treatment is performed for 10 minutes, and if the ratio of columnar crystals to the plate thickness is 75% or less, the solidified state is maintained or heavy solution treatment is performed, and then the cold rolling rate is 50 to 80. % cold rolling, and further 10
The first invention provides a method for producing an austenitic stainless steel thin plate strip, which is characterized by performing final annealing for 0.5 to IO minutes at a temperature of 00 to 1150°C, and (2) thickness of the austenitic stainless steel thin plate strip. Saha 5
Claim 1 characterized in that it is below +nm.
This invention consists of two inventions, with the second invention being the method for manufacturing an austenitic stainless steel thin plate strip described in 1.
本発明に係ろオーステナイト系ステンレスＲ４Ｒ板帯の
製造方法について、以下詳細に説明する。The method for manufacturing the austenitic stainless steel R4R plate strip according to the present invention will be described in detail below.
本発明に係ろオーステナイト系ステンレス鋼薄板帯の製
造方法において使用するオーステナイト系ステンレス鋼
としては、ＳＵＳ ３０４、ＳＵＳ ３０４Ｌ、Ｓ
ＵＳ ３１６．５ＵＳ３１６［、、ＳＵＳ ３０Ｌ
ＳＵＳ ３０２、ＳＯＳ ３２３ＳＵＳ ３
４７等があるが、これらｉｌｌ以外のオーステナイト系
ステンレス鋼をも対象とすることもできる。The austenitic stainless steels used in the method for producing thin austenitic stainless steel thin plate strips according to the present invention include SUS 304, SUS 304L, and SUS 304L.
US 316.5US316[,,SUS 30L
SUS 302, SOS 323SUS 3
47, etc., but austenitic stainless steels other than these may also be used.
本発明のオーステナイト系ステンレス鋼薄板帯の製造方
法においては、冷間圧延前の溶体化処理および冷間圧延
率を規制することにより、均一な組織が得られるもので
はあるが、従来法による場合に比較すると均一化される
機会が少ないから、凝固状態においてできるたけ各成分
を均一に分布させる必要があり、このことは、連続鋳造
急速凝固法を採用することによって可能となるものであ
る。In the method for producing an austenitic stainless steel thin plate strip of the present invention, a uniform structure can be obtained by solution treatment before cold rolling and by controlling the cold rolling rate. In comparison, there are fewer opportunities for uniformity, so it is necessary to distribute each component as uniformly as possible in the solidified state, and this is made possible by adopting the continuous casting rapid solidification method.
このような観点から、連続鋳造急速凝固条件は、自ずか
ら限定されろものであり、凝固速度としては１０°Ｃ／
ｓｅｃ以上は必要である。この凝固連間を行なうための
実際の技術としては、特に限定的ではないけれども、単
ロール法および双ロール法によるのが最も合理的である
。From this point of view, continuous casting rapid solidification conditions are naturally limited, and the solidification rate is 10°C/
sec or more is necessary. The actual technique for carrying out this coagulation process is not particularly limited, but the single roll method and the twin roll method are the most rational.
通常、急冷・凝固された薄鋳片の鋳造組織は板面の法線
方向に垂直に柱状晶が発達している場合が多く、フェラ
イト系鋼板においては、この柱状晶の成長方向は＜１０
０＞軸であることは知られているか、オーステナイト系
ステンレス鋼でら１鋳鋼片の板面の法線方向に＜１００
＞γ軸を有する結晶粒が多く認められた。Normally, the cast structure of rapidly cooled and solidified thin slabs often has columnar crystals growing perpendicular to the normal direction of the plate surface, and in ferritic steel sheets, the growth direction of these columnar crystals is <10
It is known that the austenitic stainless steel has a <100
>Many crystal grains with γ axis were observed.
従来のステンレスｗ４＠を製造する場合におけろように
、冷間圧延前に熱間圧延工程を行なう場合には、これに
よってこの柱状晶組織が破壊され、熱間圧延後の鋼板に
おいては殆ど集合組織を示していないランダムな組織と
なっている。When a hot rolling process is performed before cold rolling, as in the production of conventional stainless steel w4@, this columnar crystal structure is destroyed, and almost no aggregates appear in the steel sheet after hot rolling. It is a random organization that does not indicate the organization.
従って、このような鋼板を冷間圧延−焼鈍を行なうと、
良好な引張特性が圧延方向に依存しないで得られるが、
上記に説明したような熱間圧延工程を省略すると、＜１
００＞軸方向に成長した柱状晶の凝固組織を有する鋳片
を直接冷間圧延を行なうことになるので、たとえ、１０
００〜１１５０℃の温度において最終溶体化処理を行な
ったとしても、凝固組織に起因する不均一性（偏析）お
よび異方性が残存して、良好な機械的性質が得られない
のである。Therefore, when such a steel plate is cold rolled and annealed,
Although good tensile properties are obtained independent of the rolling direction,
If the hot rolling process as explained above is omitted, <1
00> Since the slab having a solidified structure of columnar crystals grown in the axial direction is directly cold-rolled, even if 10
Even if the final solution treatment is performed at a temperature of 00 to 1150°C, good mechanical properties cannot be obtained because of the residual non-uniformity (segregation) and anisotropy caused by the solidified structure.
しかして、鋳片の板厚方向における柱状晶の比率に対し
て、冷間圧延前の溶体化処理を行なうか、否かを決定し
、かつ、冷間圧延率を５０％以上、８０％以下に規制す
ることにより、最終溶体化焼鈍後に均一で、異方性のな
い組織が得られ、良好な機械的性質が得られる。Therefore, it is determined whether or not to perform solution treatment before cold rolling with respect to the ratio of columnar crystals in the thickness direction of the slab, and the cold rolling rate is set to 50% or more and 80% or less. By regulating this, a uniform, non-anisotropic structure can be obtained after final solution annealing, and good mechanical properties can be obtained.
また、単ロールまたは双ロールの回転表面上でオーステ
ナイト系ステンレス溶鋼を連続的に抜熱して製造される
鋳片は、柱状晶が表層から中心層に向かって成長した組
織を有しているが、ロールの冷却能力や状態によっては
中心層には等軸品が存在することがあり、これは双ロー
ルの場合には最近接点で凝固を完了しなかった溶湯が自
然凝固したものである。このような等軸晶の場合には集
合組織や偏析が存在しないため、そのまま冷間圧延−焼
鈍を行なっても、一定以上の冷間圧延率を付与すれば良
好な機械的性質が得られる。従って、冷間圧延前の溶体
化処理を行なわなくてもよい。In addition, slabs manufactured by continuously removing heat from austenitic stainless steel on the rotating surface of a single roll or twin rolls have a structure in which columnar crystals grow from the surface layer toward the center layer. Depending on the cooling capacity and condition of the rolls, equiaxed products may exist in the center layer, and in the case of twin rolls, this is the natural solidification of molten metal that has not completely solidified at the point of closest contact. In the case of such equiaxed crystals, there is no texture or segregation, so even if cold rolling and annealing are performed as is, good mechanical properties can be obtained if a cold rolling rate of a certain level or more is applied. Therefore, it is not necessary to perform solution treatment before cold rolling.
これに反して、中心まで柱状晶が成長している場合には
、これらを拡散、均一化するために冷間圧延前の溶体化
処理は不可欠のものである。このようなことは、多くの
実験を行ない、検討を行なった結果、冷間圧延前の溶体
化処理を行なう必要があるか、否かは、柱状晶の板厚に
対する比率が７５％がそのボーダーラインである。そし
て、溶体化処理は柱状晶が板厚に占める比率が７５％以
上において、１０５０〜１１５０℃の温度において２〜
１０分間行なうのがよい。なお、溶体化処理は柱状晶が
板厚に占める比率が７５％以下では行なわなくても、溶
体化処理を行なったと同様の効果か得られる。しかし、
柱状晶の比率が７５％以下の場合でも溶体化処理を行な
ってもよい。On the other hand, if columnar crystals have grown to the center, solution treatment before cold rolling is essential to diffuse and homogenize them. As a result of many experiments and studies, we have determined whether or not it is necessary to perform solution treatment before cold rolling. It's a line. Solution treatment is performed at a temperature of 1,050 to 1,150°C when the ratio of columnar crystals to the plate thickness is 75% or more.
It is best to do this for 10 minutes. Incidentally, even if the solution treatment is not performed when the ratio of columnar crystals to the plate thickness is 75% or less, the same effect as the solution treatment can be obtained. but,
Solution treatment may be performed even when the ratio of columnar crystals is 75% or less.
冷間圧延率は良好な機械的性質を得ろための重要な要素
であり、冷間圧延を行なわないものは勿論、冷間圧延率
が５０％未満では最終焼鈍時に均一な再結晶核生成を期
待することができず、そのため、凝固組織の偏析、不均
一性に対応した核生成が発生し、異方性の大きい劣悪な
機械的性質しか得られない。従って、これを解決するた
めには５０％以上の冷間圧延を行なう必要があり、また
、８０％を越える冷間圧延率では過度の冷間圧延歪を与
えるし、再結晶核生成サイト数の増加に伴い、最終焼鈍
後に得られる組織の結晶粒が微細化するばかりか、冷間
圧延集合組織の形成に伴い、集合組織を有する再結晶組
織が生成されるため、異方性の大きい、低い伸びしか得
られないのである。Cold rolling rate is an important factor to obtain good mechanical properties, and uniform recrystallization nucleation is expected during final annealing when the cold rolling rate is less than 50%, as well as those without cold rolling. Therefore, nucleation corresponding to segregation and non-uniformity of the solidified structure occurs, resulting in poor mechanical properties with large anisotropy. Therefore, in order to solve this problem, it is necessary to perform cold rolling of 50% or more, and cold rolling of more than 80% causes excessive cold rolling strain and reduces the number of recrystallization nucleation sites. As the increase in temperature increases, not only the crystal grains of the structure obtained after the final annealing become finer, but also a recrystallized structure with a texture is generated with the formation of a cold rolling texture, resulting in large or low anisotropy. All you can get is growth.
最終焼鈍が１０００℃未満の温度および０．５分未満の
時間では再結晶したオーステナイト粒が得られず、また
、１１５０℃を越える温度および１０分を越える時間で
は結晶粒が異常に粗大化し、良好な機械的性質が得られ
ないのである。If the final annealing is performed at a temperature of less than 1000°C and for a time of less than 0.5 minutes, recrystallized austenite grains will not be obtained, and if the final annealing is performed at a temperature of over 1150°C and for a time of more than 10 minutes, the crystal grains will become abnormally coarse. Therefore, good mechanical properties cannot be obtained.
［実 施 例］
本発明に係るオーステナイト系ステンレス鋼薄板帯の製
造方法の実施例を説明する。[Example] An example of the method for manufacturing an austenitic stainless steel thin plate strip according to the present invention will be described.
実施例
第１表に示す５ＵＳ３０４ｊＩ４の薄鋼帯を銅合金製ロ
ール（Ｃ１）およびステンレス製ロール（Ｃ２）を有す
る双ロールキャスターによって製造した。第１図に示す
銅合金製双ロールによって製造した薄鋼帯（ａ）は、中
心層まで柱状晶組織であるが、ステンレス製双ロールに
よって製造した薄鋼帯（ｂ）は表面層は柱状晶であるが
、中心層には等軸晶が存在し、その比率は約３０％であ
る。板厚は何れも１ 、８ ｍｍである。EXAMPLES Thin steel strips of 5US304jI4 shown in Table 1 were manufactured using a twin roll caster having a copper alloy roll (C1) and a stainless steel roll (C2). The thin steel strip (a) produced using twin rolls made of copper alloy shown in Fig. 1 has a columnar crystal structure up to the center layer, but the thin steel strip (b) produced using twin rolls made of stainless steel has a columnar crystal structure in the surface layer. However, equiaxed crystals exist in the central layer, and their ratio is about 30%. The thickness of each plate is 1.8 mm.
次に、上記の薄鋼帯の一部にはそのまま０〜８５％の冷
間圧延率で冷間圧延を行ない、さらに、１１００℃の温
度において３分間の最終焼鈍を行なった。Next, a part of the thin steel strip was subjected to cold rolling as it was at a cold rolling rate of 0 to 85%, and was further subjected to final annealing at a temperature of 1100° C. for 3 minutes.
第２表に銅合金製ロールのにより製造したステンレス系
薄鋼帯および第３表にステンレス製ロールにより製造し
たステンレス系薄鋼帯に、最終焼鈍後の圧延方向に対し
て、平行、４５°および直角の３方向についての引張試
験結果を示す。Table 2 shows the stainless steel thin steel strips produced with copper alloy rolls, and Table 3 shows the stainless steel strips produced with stainless steel rolls, parallel to the rolling direction after final annealing, 45° and The tensile test results in three orthogonal directions are shown.
本発明に係るオーステナイト系ステンレス鋼薄板帯の製
造方法により製造した、ステンレス薄帯の０．２％耐力
（ｋｇｆ／ｍｍ”）、引張強さ（Ｔ Ｓ ：ｋｇｆ／ｍ
ｍ”）、伸び（Ｅｌ：％）は、引張力向による差が小さ
く、かつ、良好な効果を示していることがわかる。The 0.2% yield strength (kgf/mm") and tensile strength (T S :kgf/m
It can be seen that there are small differences in elongation (El: %) depending on the direction of tensile force, and that good effects are exhibited.
［発明の効果］
以上説明したように、本発明に係るオーステナイト系ス
テンレス鋼薄板帯の製造方法は上記の構成であるから、
異方性か小さ（、かつ、優れた機賊的性質を有するオー
ステナイト系ステンレス鋼薄板帯を効率よく製造するこ
とができるという効果を有するものである。[Effects of the Invention] As explained above, since the method for manufacturing an austenitic stainless steel thin plate strip according to the present invention has the above configuration,
This method has the effect that an austenitic stainless steel thin plate strip having low anisotropy (and excellent mechanical properties) can be efficiently manufactured.
第１図（ａ）は銅合金製ロールにより製造されたオース
テナイト系ステンレス鋼薄帯の顕微鏡写真、第１図（ｂ
）はステンレス鋼製ロールにより製造されたオーステナ
イト系ステンレス鋼薄帯の顕微鏡写真である。
手続補正古（方式）
事件の表示
昭和６３年特許願第２１４３４４号
発明の名称
オーステナイト系ステンレスｊｉｌ／１１ｔ、ｌＩｉ仮
帯の製造方法
補正をする者
事件との関係 特許出願人
住所 神戸市中央区脇浜町１丁目３番１８号名称 （１
１９）株式会社神戸製鋼所（外１名）代表者 亀高素占Figure 1(a) is a micrograph of an austenitic stainless steel ribbon produced using a copper alloy roll, and Figure 1(b)
) is a micrograph of an austenitic stainless steel ribbon produced using a stainless steel roll. Old procedure amendment (method) Display of the case 1986 Patent Application No. 214344 Name of the invention Person who amends the manufacturing method of austenitic stainless steel jil/11t, LIi temporary band Relationship with the case Patent applicant address Wakihama, Chuo-ku, Kobe City Town 1-3-18 Name (1
19) Kobe Steel, Ltd. (1 other person) Representative: Motaka Kametaka
Claims (2)
表面上において、オーステナイト系ステンレス鋼を連続
的に急冷・凝固することにより薄板帯を製造し、次いで
、この薄板帯の凝固組織が柱状晶で板厚に占める比率が
７５％以上の場合には、１０５０〜１１５０℃の温度に
おいて２〜１０分の溶体化処理を行ない、また、柱状晶
の板厚に占める比率が７５％以下であれば凝固状態のま
まか、或いは、前記溶体化処理を行ない、その後、冷間
圧延率５０〜８０％の冷間圧延を行ない、さらに、１０
００〜１１５０℃の温度において０．５〜１０分の最終
焼鈍を行なうことを特徴とするオーステナイト系ステン
レス鋼薄板帯の製造方法。(1) A thin plate is manufactured by continuously rapidly cooling and solidifying austenitic stainless steel on the rotating surface of one type of roll, either a single roll or a twin roll, and then the solidified structure of this thin plate is If the ratio of columnar crystals to the plate thickness is 75% or more, solution treatment is performed at a temperature of 1050 to 1150°C for 2 to 10 minutes, and if the ratio of columnar crystals to the plate thickness is 75% or less, If any, the solidified state is maintained or the solution treatment is performed, and then cold rolling is performed at a cold rolling rate of 50 to 80%, and further 10
1. A method for producing an austenitic stainless steel thin plate strip, comprising final annealing for 0.5 to 10 minutes at a temperature of 00 to 1150°C.
ｍｍ以下であることを特徴とする特許請求の範囲第１項
記載のオーステナイト系ステンレス鋼薄板帯の製造方法
。(2) The thickness of the austenitic stainless steel thin plate strip is 5
2. The method for producing an austenitic stainless steel thin plate strip according to claim 1, wherein the thickness is less than mm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21434488A JPH0261007A (en) | 1988-08-29 | 1988-08-29 | Production of austenitic stainless steel foil |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21434488A JPH0261007A (en) | 1988-08-29 | 1988-08-29 | Production of austenitic stainless steel foil |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH0261007A true JPH0261007A (en) | 1990-03-01 |
Family
ID=16654209
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21434488A Pending JPH0261007A (en) | 1988-08-29 | 1988-08-29 | Production of austenitic stainless steel foil |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0261007A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0273917A (en) * | 1988-09-07 | 1990-03-13 | Nippon Yakin Kogyo Co Ltd | Manufacture of austenitic stainless steel thin sheet having good workability |
-
1988
- 1988-08-29 JP JP21434488A patent/JPH0261007A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0273917A (en) * | 1988-09-07 | 1990-03-13 | Nippon Yakin Kogyo Co Ltd | Manufacture of austenitic stainless steel thin sheet having good workability |
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