JPS6369921A - Production of ferritic stainless steel sheet having excellent formability and ridging resistance - Google Patents
Production of ferritic stainless steel sheet having excellent formability and ridging resistanceInfo
- Publication number
- JPS6369921A JPS6369921A JP21243086A JP21243086A JPS6369921A JP S6369921 A JPS6369921 A JP S6369921A JP 21243086 A JP21243086 A JP 21243086A JP 21243086 A JP21243086 A JP 21243086A JP S6369921 A JPS6369921 A JP S6369921A
- Authority
- JP
- Japan
- Prior art keywords
- rolling
- stainless steel
- ferritic stainless
- sheet
- ridging resistance
- 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
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 19
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000005096 rolling process Methods 0.000 claims abstract description 62
- 238000005098 hot rolling Methods 0.000 claims abstract description 22
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 abstract description 20
- 238000000137 annealing Methods 0.000 abstract description 11
- 229910052804 chromium Inorganic materials 0.000 abstract description 2
- 238000009826 distribution Methods 0.000 abstract description 2
- 239000000463 material Substances 0.000 abstract description 2
- 229910000831 Steel Inorganic materials 0.000 description 10
- 239000010959 steel Substances 0.000 description 10
- 238000005097 cold rolling Methods 0.000 description 5
- 238000002474 experimental method Methods 0.000 description 5
- 230000007423 decrease Effects 0.000 description 4
- 238000010586 diagram Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000011835 investigation Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 229910052757 nitrogen Inorganic materials 0.000 description 3
- 230000007547 defect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 101100165177 Caenorhabditis elegans bath-15 gene Proteins 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000003796 beauty Effects 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000011179 visual inspection Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野〕
本発明は成形加工性および耐リジング性に優れたフェラ
イト系ステンレス鋼板の製造方法に関する。DETAILED DESCRIPTION OF THE INVENTION [Field of Industrial Application] The present invention relates to a method for manufacturing a ferritic stainless steel sheet having excellent formability and ridging resistance.
一般にフェライト系ステンレス鋼板は成分として重量比
にてｃｒ、１０〜２０％、Ｃ：０．１％以下、Ｓｉ：
１％以下、Ｍｎ：１％以下を含有し、この他に耐食性
、耐酸化性、成形加工性等の向上を目的としてＴｉ、Ｎ
ｂ、Ｍｏ、Ａｊ等の金属元素が添加される。In general, ferritic stainless steel sheets have a weight ratio of Cr: 10 to 20%, C: 0.1% or less, Si:
1% or less, Mn: 1% or less, and also contains Ti and N for the purpose of improving corrosion resistance, oxidation resistance, moldability, etc.
Metal elements such as b, Mo, and Aj are added.
フェライト系ステンレス冷延鋼板は熱間圧延、冷間圧延
に引続き仕上焼鈍することによって製造され、家庭用具
、自動車部品、厨房用品などに広く使用されている。し
かしながら、これらの製品化に当り、フェライト系ステ
ンレス鋼板をプレス成形するとりジングとよばれる圧延
方向に沿った特有の凹凸が発生し易く、これによって成
形品の表面の美麗さが著しく損なわれる。このため成形
加工性に優れかつリジングの発生を防止することがフェ
ライト系ステンレス鋼板を製造する上で大きな課題とな
っている。Ferritic stainless steel cold-rolled steel sheets are manufactured by hot rolling, cold rolling, and final annealing, and are widely used in household appliances, automobile parts, kitchen utensils, and the like. However, when producing these products by press forming a ferritic stainless steel plate, unique irregularities along the rolling direction called sludges tend to occur, which significantly impairs the beauty of the surface of the molded product. For this reason, it is a major issue in manufacturing ferritic stainless steel sheets to have excellent formability and to prevent the occurrence of ridging.
従来からりジング発生の防止を目的とした製造工程上の
方策がいくつか施されている。例えば（イ）オーステナ
イト相生成元素量の増加、（０）炭窒化物形成元素の添
加、（）１）スラブ加熱温度の低下、（ニ）熱間圧延温
度の低下、（ホ）熱間における大圧下圧延、（へ）高温
熱処理、（ト）２回圧延の実施等の対策が一般に行われ
ているが、以上のような方法によってもリジングの発生
を完全に防止することは困難である。また、上記の対策
によってコストアップ、設備寿命の短縮、あるいは生産
性の低下等の問題を招いている。Conventionally, several measures have been taken in the manufacturing process to prevent the occurrence of karasing. For example, (a) increase in the amount of austenite phase forming elements, (0) addition of carbonitride forming elements, (1) decrease in slab heating temperature, (d) decrease in hot rolling temperature, (e) increase in hot rolling temperature. Countermeasures such as reduction rolling, (f) high-temperature heat treatment, and (g) double rolling are generally taken, but even with the above methods, it is difficult to completely prevent the occurrence of ridging. Furthermore, the above measures have led to problems such as increased costs, shortened equipment life, and decreased productivity.
更に、鋼板からプレス成形により製品を得る場合、成形
加工性の面内異方性が大きな問題となる。Furthermore, when a product is obtained from a steel plate by press forming, in-plane anisotropy in forming processability becomes a major problem.
すなわち、一般に鋼板は面内で異方性が存在し、その差
が大きいと深絞り加工を行った場合に各方向での変形能
が違うために、フランジの各方向での大小あるいは深絞
り加工前の板取りの点で歩留りが低下しコストアップに
なる。In other words, steel plates generally have in-plane anisotropy, and if the difference is large, the deformability in each direction will be different when deep drawing is performed. The previous blanking reduces yield and increases costs.
熱延におけろ圧下率の増加による耐リジング性向上を目
的とした従来技術では、例えば特開昭５７−７０２３４
は、フェライト系ステンレス鋼の熱間圧延での粗圧延開
始温度を１１５０℃以下とし、次いで連続仕上熱延での
圧下開始温度を９００℃以上とし、仕上熱延での圧下率
が少なくとも２５％である圧延を複数バス行う方法を開
示している。一方、耐リジング性およびプレス成形性の
向上を目的としたものとして、特公昭５９−４３９７７
は、ＡＩを含有するフェライト系ステンレス鋼の熱間圧
延においてスラブを９００〜１２００℃の温度に加熱後
１バス当り２０％以上の圧下を１バス以上行う熱間圧延
を行った後、連続焼鈍を行う方法を開示している。Conventional techniques aimed at improving ridging resistance by increasing the reduction ratio in hot rolling include, for example, Japanese Patent Application Laid-Open No. 57-70234.
The rough rolling start temperature in hot rolling of ferritic stainless steel is 1150°C or lower, the rolling start temperature in continuous finishing hot rolling is 900°C or higher, and the rolling reduction in finishing hot rolling is at least 25%. A method for performing a certain rolling process using multiple buses is disclosed. On the other hand, for the purpose of improving ridging resistance and press formability, Japanese Patent Publication No. 59-43977
In the hot rolling of ferritic stainless steel containing AI, after heating the slab to a temperature of 900 to 1200 ° C., hot rolling is performed in which a reduction of 20% or more is performed in one or more baths per bath, and then continuous annealing is performed. Discloses how to do so.
以上の方法は、熱延におけるスラブ加熱を低温で行い、
仕上圧延で１バスあるいは複数バスの強圧下圧延を行う
ことにより熱延中での熱延組織の再結晶化を促進し、耐
リジング性および成形加工性の向上を図ることを目的と
している。The above method heats the slab in hot rolling at a low temperature,
The purpose of this is to promote recrystallization of the hot-rolled structure during hot rolling by carrying out one or more passes of strong reduction rolling in finish rolling, thereby improving ridging resistance and formability.
一方、このような方法の実用化においては、次の問題が
ある。すなわち、スラブ加熱温度の低下により、仕上圧
延における各バスの圧延温度が低下しロール負荷が増大
するために、ロール焼付等による鋼板の表面欠陥の発生
およびロール交換頻度の増加等の問題を生じろために、
耐リジング性、成形加工性を向上させるべく圧延温度の
低下および圧下率増加は商用の大量生産工程では困難で
ある。従って実用上熱延工程では、耐リジング性、成形
加工性の向上に不適である比較的高温でのスラブ加熱、
仕上圧延での軽圧下バススケジュールによる圧延がやむ
を得ず行われている。On the other hand, there are the following problems in practical application of such a method. In other words, due to a decrease in slab heating temperature, the rolling temperature of each bath in finish rolling decreases and the roll load increases, resulting in problems such as occurrence of surface defects on the steel plate due to roll seizure and an increase in the frequency of roll replacement. for,
Lowering the rolling temperature and increasing the reduction rate in order to improve ridging resistance and moldability are difficult in commercial mass production processes. Therefore, in practical hot rolling processes, slab heating at a relatively high temperature, which is unsuitable for improving ridging resistance and formability, is required.
It is unavoidable that finishing rolling is carried out using a light reduction bus schedule.
本発明の目的は、上記従来技術の問題点を解決し、リジ
ングの発生がなく成形加工性に優れたフェライト系ステ
ンレス鋼板の実用的な製造方法を提供するにある。An object of the present invention is to solve the problems of the prior art described above and to provide a practical method for manufacturing a ferritic stainless steel sheet that does not cause ridging and has excellent formability.
〔問題点を解決するための手段および作用〕本発明の要
旨とするところは次の如（である。[Means and operations for solving the problems] The gist of the present invention is as follows.
すなわち、熱間圧延におけるスラブ加熱を１２００℃を
越え１３００℃以下の温度範囲で行う段階と、粗圧延終
了後の複数回の圧延バスから成る仕上圧延工程において
最終バスの圧下率が１５〜３５％の範囲および仕上圧延
終了温度が８００〜９５０℃の範囲で熱間圧延を行う段
階と、を有して成ることを特徴とする成形加工性および
耐リジング性に優れたフェライト系ステンレス鋼板の製
造方法である。That is, in the step of hot rolling where the slab is heated in a temperature range exceeding 1200°C and below 1300°C, and in the finishing rolling process which consists of multiple rolling baths after rough rolling, the reduction ratio of the final bath is 15 to 35%. A method for producing a ferritic stainless steel sheet with excellent formability and ridging resistance, comprising the steps of hot rolling at a temperature in the range of 800 to 950°C at the end of finishing rolling. It is.
次に本発明の基礎になった実験について説明する。真空
小型溶解炉でＣ：０．０６％、Ｓｉ：０４１％、Ｍｎ：
０．５２％、Ｐ：０．０２１％、Ｓ：０．００７％、Ｎ
ｉ：０．０７％、Ｃｒ：１６３８％、Ａｊ：０．００９
％、Ｎ：０．０２１％の成分の小型鋼塊を実験室的に溶
製し、鋼塊を１２５０℃に加熱し、２５１ｗ１１厚に粗
圧延を行った後、第１表の各種の条件で仕上圧延を行い
引続き８５０℃Ｘ４ｈｒの熱延板焼鈍を行った後、１回
冷延法で０．７ｍ厚に冷間圧延し、８５０℃×３Ｏ８の
仕上焼鈍を行って冷延板を製作した。Next, the experiments that formed the basis of the present invention will be explained. C: 0.06%, Si: 041%, Mn:
0.52%, P: 0.021%, S: 0.007%, N
i: 0.07%, Cr: 1638%, Aj: 0.009
%, N: A small steel ingot with a composition of 0.021% was melted in a laboratory, the steel ingot was heated to 1250°C, and after rough rolling to a thickness of 251w11, it was rolled under the various conditions shown in Table 1. After finish rolling and subsequently annealing the hot rolled plate at 850°C for 4 hours, it was cold rolled once to a thickness of 0.7 m using a cold rolling method, and finished annealing at 850°C x 3O8 to produce a cold rolled plate. .
かくして得られた各冷延板の成形加工性と耐りジング性
に対する調査結果を第１図および第２図に示した。なお
、成形性の指標であるｒ値はＬ方向（圧延方向に平行）
、Ｃ方向（圧延方向に垂直）、Ｄ方向（圧延方向に４５
度）のｒ値の平均値性の指標は
リジングの指標としてのりジングうねり高さは冷延仕上
焼鈍板から圧延方向に採取した引張試験片に２０％の引
張歪を与え、発生したりジングのうねり高さを表面粗度
計で測定した。耐リジング性は目視による官能的な評価
が一般的であるが、これはりジングうねり高さの測定値
とよく一致し、うねり高さの増加と共にリジングの度合
は劣化する。しかし、リジングのうねり高さが１０μｍ
以下の場合は目視によろりジングの発生は認められず、
極めて優れた耐リジング性の評価を受ける。The results of the investigation on the formability and jing resistance of each cold-rolled sheet thus obtained are shown in FIGS. 1 and 2. Note that the r value, which is an index of formability, is in the L direction (parallel to the rolling direction).
, C direction (perpendicular to the rolling direction), D direction (45 in the rolling direction)
The average value of the r-value of the cold rolled finish annealed sheet is used as an index of ridging. The waviness height was measured using a surface roughness meter. The ridging resistance is generally evaluated visually and visually, and this agrees well with the measured value of the ridging waviness height, and the degree of ridging deteriorates as the waviness height increases. However, the undulation height of ridging is 10 μm.
In the following cases, no occurrence of rolling is observed by visual inspection.
Evaluated for extremely excellent ridging resistance.
第１図は仕上圧延における最終バスの圧下率と△ｒ値、
７値およびリジングのうねり高さとの関係を示したもの
で、最終圧下率が１５％以上になると成形加工性、耐リ
ジング性が極めて良好であり、仕上圧延全体の圧下率が
同等であっても、最終バスでの圧下率の上昇により特性
が向上することを示している。Figure 1 shows the rolling reduction ratio and △r value of the final bath in finish rolling,
7 value and the waviness height of ridging. It shows that when the final rolling reduction is 15% or more, the formability and ridging resistance are extremely good, and even if the rolling reduction of the entire finish rolling is the same. , which shows that the characteristics improve with an increase in the rolling reduction in the final bath.
第 １ 表
上段 圧下率（％）
最終バスの圧下率が３０％である水準Ａ６は、最終バス
の圧下率が７％で１〜４バス目までが３０％である水準
Ａ１にくらべ特性が著しく優れている。Table 1 Upper row Reduction ratio (%) Level A6, in which the reduction ratio in the final bath is 30%, has significantly better characteristics than level A1, in which the reduction ratio in the final bath is 7% and 30% in the first to fourth baths. Are better.
仕上圧延における最終バスは、圧延温度が比較的低く、
熱間加工性の低下によるロールの焼付き等の欠陥が生じ
易いこと、最終バスは鋼板の表面性状におよぼす影響が
大きいことなどから、一段には１５％未満の軽圧下が行
われているが、本実験の結果から最終バスでの圧下率の
上昇が耐リジング性の向上に極めて有効であることが判
明した。The final bath in finish rolling has a relatively low rolling temperature.
Light reduction of less than 15% is carried out because defects such as roll seizure are likely to occur due to reduced hot workability, and the final bath has a large effect on the surface properties of the steel sheet. The results of this experiment revealed that increasing the rolling reduction in the final bath is extremely effective in improving ridging resistance.
一方、最終バスの圧下率が３５％を越えても特性向上の
効果は飽和し、かえってロールへの負荷が増大するだけ
であるので３５％以下が望ましい。On the other hand, even if the rolling reduction ratio of the final bath exceeds 35%, the effect of improving properties will be saturated and the load on the rolls will only increase, so it is desirable that the rolling reduction ratio be 35% or less.
第２図は仕上圧延終了温度と△ｒ１下値およびリジング
うねり高さとの関係を示したもので、仕上圧延終了温度
が８００℃以上９５０℃以下で極めて良好な成形加工性
および削りジング性が得られろ。Figure 2 shows the relationship between finish rolling finish temperature, △r1 lower value, and ridging waviness height, and shows that extremely good formability and machinability can be obtained when finish rolling finish temperature is 800°C or higher and 950°C or lower. reactor.
従って仕上圧延の最終バスの圧下率が１５〜３５％で仕
上圧延終了温度が８００〜９５０℃であれば、表面性状
に優れ、かつ成形加工性、耐リジング性に優れた鋼板が
得られるが、実際の大量生産工程への適用にあたっては
、ロール負荷の低減といった理由からより高温での圧延
が好ましい。Therefore, if the reduction ratio in the final bath of finish rolling is 15 to 35% and the finish rolling end temperature is 800 to 950°C, a steel plate with excellent surface texture, formability, and ridging resistance can be obtained. When applied to an actual mass production process, rolling at a higher temperature is preferred for the reason of reducing roll load.
そのためには、スラブ加熱温度をより高温にする必要を
生じるが、スラブ加熱温度の上昇は成形加工性、耐リジ
ング性の劣化の問題を生じる。For this purpose, it is necessary to raise the slab heating temperature to a higher temperature, but an increase in the slab heating temperature causes problems of deterioration of moldability and ridging resistance.
そこで、以上の基礎となった実験について、更にスラブ
加熱温度と仕上圧延バススケジュールに関しての実験を
行ったので、この実験について説明する。Therefore, in addition to the above-mentioned basic experiment, we conducted an experiment regarding slab heating temperature and finish rolling bus schedule, and this experiment will be explained below.
上記と同様の成分の小型鋼塊を用いてスラブ加熱温度を
１０５０〜１３５０℃に変化させ仕上圧延を第１表の水
準Ａｌ（最終バス７％）、Ａ３（最終バス１５％）およ
びＡ６（最終バス３０％）の条件で行い、引続き８５０
℃×４ｈｒの熱延板焼鈍を行った後１回冷延法で０．７
ｍｒａ厚に冷間圧延し、８５０℃×３Ｏ８の仕上焼鈍を
行って冷延板を作成した。かくして得られた各冷延板の
成形性と耐すジング性に対する調査結果を第３図に示し
た。Using a small steel ingot with the same composition as above, the slab heating temperature was varied from 1050 to 1350°C, and finish rolling was carried out at the levels Al (7% final bath), A3 (15% final bath), and A6 (final bath 15%) as shown in Table 1. bus (30%), and continue with 850
After hot-rolled sheet annealing for 4 hours at
A cold rolled sheet was prepared by cold rolling to mra thickness and final annealing at 850°C x 3O8. The results of the investigation on the formability and jing resistance of each cold-rolled sheet thus obtained are shown in FIG.
第３図において、スラブ加熱温度の上昇によりＴ値、耐
リジング性とも劣化する傾向にあるが、その挙動は仕上
圧延バススケジュールによって異なる。最終バスの圧下
率が７％（水準ＡＩ）の場合では、スラブ加熱温度が１
１５０℃を越えると７値、耐リジング性とも著しく劣化
するが、最終バスの圧下率が１５％（水準Ａ３）、３０
％（水準Ａ６）の場合は、スラブ加熱温度が１３００℃
以下で優れた特性が得られる。すなわち、スラブ加熱温
度の上昇による特性の劣化はスラブ加熱温度が１３００
℃以下であれば、最終バスの圧下率を１５％以上とする
仕上圧延の圧下率配分により克服され著しく優れたＴ値
および耐リジング性が得られることがわかる。In FIG. 3, both the T value and the ridging resistance tend to deteriorate as the slab heating temperature increases, but the behavior differs depending on the finish rolling bus schedule. When the final bath reduction rate is 7% (level AI), the slab heating temperature is 1
When the temperature exceeds 150℃, both the 7 value and the ridging resistance deteriorate significantly, but the final bath reduction rate is 15% (level A3) and 30%.
% (level A6), the slab heating temperature is 1300℃
Excellent properties can be obtained with: In other words, the deterioration of characteristics due to an increase in the slab heating temperature occurs when the slab heating temperature is 1300
℃ or less, it is found that extremely excellent T value and ridging resistance can be obtained, which can be overcome by distributing the rolling reduction in the finish rolling such that the rolling reduction in the final bath is 15% or more.
一方、Δｒ値については、スラブ加熱温度が１２００℃
を越えると良好であるが、１２００℃以下で著しく劣化
する。更にスラブ加熱温度が１２００℃を越えて最終バ
スの圧下率が１５％（水準Ａ３） 、３０％（水準Ａ６
）の場合は著しく良好である。On the other hand, regarding the Δr value, the slab heating temperature is 1200℃
It is good when the temperature exceeds 1200°C, but it deteriorates significantly below 1200°C. Furthermore, when the slab heating temperature exceeds 1200℃, the reduction rate of the final bath is 15% (level A3) and 30% (level A6).
) is significantly better.
本発明においては上記の実験結果に基づきスラブ加熱温
度を１２００℃を越え１３００℃以下の温度範囲に、仕
上圧延工程での最終バスの圧下率を１５〜３５％の範囲
に、仕上圧延終了１度を８００〜９５０℃の範囲に限定
した。In the present invention, based on the above experimental results, the slab heating temperature is set to a temperature range exceeding 1200°C and below 1300°C, the rolling reduction rate of the final bath in the finish rolling process is set to a range of 15 to 35%, and once the finish rolling is completed, was limited to a range of 800 to 950°C.
第２表に化学成分を示したＡ鋼、ＢＨ３およびＣ鋼のｓ
ｍ種のフェライト系ステンレス鋼の連鋳スラブを４■厚
に熱間圧延後、０．７ｍｒｒ厚に１回冷延法で冷延した
。その具体的実施条件および冷延仕上焼鈍後の耐リジン
グ性、成形加工性の調査結果を第３表に示した。s of A steel, BH3 and C steel whose chemical compositions are shown in Table 2
A continuously cast slab of type m ferritic stainless steel was hot rolled to a thickness of 4mm, and then cold rolled once to a thickness of 0.7mrr using a cold rolling method. Table 3 shows the specific implementation conditions and the investigation results of ridging resistance and moldability after cold rolling finish annealing.
第 ２ 表
第３表において、５ＵＳ４１０ＳＳＵＳ４３０フエライ
ト系ステンレス鋼に対して、熱延板焼鈍を長時間焼純、
短時間焼鈍あるいは焼鈍を省略した場合に、本発明によ
る熱間圧延スケジュールによればリジングのうねり高さ
がいずれも１０μｍ以下で耐リジング性が極めて優れ、
かつ成形加工性も優れていることが明らかである。Table 2 In Table 3, 5US410SSUS430 ferritic stainless steel was hot-rolled plate annealed for a long time,
When short-time annealing or annealing is omitted, according to the hot rolling schedule according to the present invention, the ridging waviness height is all 10 μm or less, and the ridging resistance is extremely excellent.
It is also clear that the molding processability is excellent.
本発明は上記実施例からも明らかな如く、スラブ加熱温
度と熱間圧延におけるスケジュール、特に仕上圧延の圧
下率配分と圧延温度の限定により、成形加工性および耐
リジング性に飛躍的に優れたフェライト系ステンレス鋼
板を大量生産工程で製造する効果を挙げることができた
。As is clear from the above examples, the present invention provides a ferrite material with dramatically superior formability and ridging resistance by limiting the slab heating temperature and hot rolling schedule, especially the reduction ratio distribution in finish rolling and the rolling temperature. It was possible to produce stainless steel sheets using a mass production process.
第１図は熱間仕上圧延における最終バスの圧下率と成形
加工性および耐リジング性との関係を示す線図、第２図
は熱間圧延における仕上圧延終了温度と成形加工性およ
び耐リジング性との関係を示す線図、第３図は熱間圧延
のスラブ加熱温度と成形加工性および耐リジング性との
関係を示す線図である。Figure 1 is a diagram showing the relationship between final bath rolling reduction, formability and ridging resistance in hot finish rolling, and Figure 2 is a diagram showing the relationship between finish rolling end temperature, formability and ridging resistance in hot rolling. FIG. 3 is a diagram showing the relationship between hot rolling slab heating temperature, moldability and ridging resistance.
Claims (1)
１３００℃以下の温度範囲で行う段階と、粗圧延終了後
の複数回の圧延バスから成る仕上圧延工程において最終
バスの圧下率が１５〜３５％の範囲および仕上圧延終了
温度が８００〜９５０℃の範囲で熱間圧延を行う段階と
、を有して成ることを特徴とする成形加工性および耐リ
ジング性に優れたフェライト系ステンレス鋼板の製造方
法。(1) During hot rolling, the slab is heated in a temperature range exceeding 1,200°C and below 1,300°C, and in the finishing rolling process, which consists of multiple rolling baths after rough rolling, the reduction ratio of the final bath is 15 to 35. manufacturing a ferritic stainless steel sheet with excellent formability and ridging resistance, comprising the step of hot rolling in a range of 800 to 950° C. and a finish rolling end temperature of 800 to 950°C. Method.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21243086A JPS6369921A (en) | 1986-09-09 | 1986-09-09 | Production of ferritic stainless steel sheet having excellent formability and ridging resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP21243086A JPS6369921A (en) | 1986-09-09 | 1986-09-09 | Production of ferritic stainless steel sheet having excellent formability and ridging resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPS6369921A true JPS6369921A (en) | 1988-03-30 |
Family
ID=16622466
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP21243086A Pending JPS6369921A (en) | 1986-09-09 | 1986-09-09 | Production of ferritic stainless steel sheet having excellent formability and ridging resistance |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6369921A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012173272A1 (en) | 2011-06-16 | 2012-12-20 | 新日鐵住金ステンレス株式会社 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6024325A (en) * | 1983-07-19 | 1985-02-07 | Kawasaki Steel Corp | Production of ferritic stainless steel plate having less ridging and excellent formability |
-
1986
- 1986-09-09 JP JP21243086A patent/JPS6369921A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS6024325A (en) * | 1983-07-19 | 1985-02-07 | Kawasaki Steel Corp | Production of ferritic stainless steel plate having less ridging and excellent formability |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2012173272A1 (en) | 2011-06-16 | 2012-12-20 | 新日鐵住金ステンレス株式会社 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
| KR20140014275A (en) | 2011-06-16 | 2014-02-05 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
| KR20150084074A (en) | 2011-06-16 | 2015-07-21 | 닛폰 스틸 앤드 스미킨 스테인레스 스틸 코포레이션 | Ferritic stainless-steel sheet with excellent non-ridging property and process for producing same |
| US9771640B2 (en) | 2011-06-16 | 2017-09-26 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic stainless steel plate which has excellent ridging resistance and method of production of same |
| US10358707B2 (en) | 2011-06-16 | 2019-07-23 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic stainless steel plate which has excellent ridging resistance and method of production of same |
| US10513763B2 (en) | 2011-06-16 | 2019-12-24 | Nippon Steel & Sumikin Stainless Steel Corporation | Ferritic stainless steel plate which has excellent ridging resistance and method of production of same |
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