JPH01157743A - Production of high corrosion resistant ferritic super stainless steel strip - Google Patents
Production of high corrosion resistant ferritic super stainless steel stripInfo
- Publication number
- JPH01157743A JPH01157743A JP31518687A JP31518687A JPH01157743A JP H01157743 A JPH01157743 A JP H01157743A JP 31518687 A JP31518687 A JP 31518687A JP 31518687 A JP31518687 A JP 31518687A JP H01157743 A JPH01157743 A JP H01157743A
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- strip
- stainless steel
- molten steel
- composition
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- Granted
Links
- 230000007797 corrosion Effects 0.000 title claims abstract description 20
- 238000005260 corrosion Methods 0.000 title claims abstract description 20
- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 14
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 12
- 239000010935 stainless steel Substances 0.000 title claims description 6
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 19
- 239000010959 steel Substances 0.000 claims abstract description 19
- 238000001816 cooling Methods 0.000 claims abstract description 18
- 238000000034 method Methods 0.000 claims abstract description 16
- 229910001182 Mo alloy Inorganic materials 0.000 claims abstract description 14
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 6
- 229910052802 copper Inorganic materials 0.000 claims abstract description 5
- 239000000203 mixture Substances 0.000 claims description 13
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 7
- 239000010949 copper Substances 0.000 claims 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract description 10
- 229910052804 chromium Inorganic materials 0.000 abstract description 9
- 229910052759 nickel Inorganic materials 0.000 abstract description 2
- 238000005098 hot rolling Methods 0.000 description 6
- 238000005096 rolling process Methods 0.000 description 5
- 238000004804 winding Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 4
- 239000000126 substance Substances 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 238000000137 annealing Methods 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000010586 diagram Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005728 strengthening Methods 0.000 description 2
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 229910045601 alloy Inorganic materials 0.000 description 1
- 239000000956 alloy Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 239000004566 building material Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 238000005536 corrosion prevention Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 150000004767 nitrides Chemical class 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000003507 refrigerant Substances 0.000 description 1
- 239000013535 sea water Substances 0.000 description 1
- 238000009966 trimming Methods 0.000 description 1
Abstract
Description
【発明の詳細な説明】
(産業上の利用分野)
高純度フェライト系ステンレス鋼は、Clイオンを含む
環境での応力腐食割れに強いという特長をもち、冷蔵・
冷凍庫の内外装、建材、化学プラント、熱交換チューブ
などに用いられる。[Detailed Description of the Invention] (Field of Industrial Application) High-purity ferritic stainless steel has the feature of being resistant to stress corrosion cracking in environments containing Cl ions, and is
Used for the interior and exterior of freezers, building materials, chemical plants, heat exchange tubes, etc.
通常のフェライト系ステンレス鋼は、応力腐食割れに強
いが耐食性、機械的性質、溶接性に劣るため、応用が限
られる。Ordinary ferritic stainless steel is resistant to stress corrosion cracking, but has poor corrosion resistance, mechanical properties, and weldability, which limits its applications.
近年C,Nを極度に低減(代表的にはC≦0.030w
t%(以下単に%で示す)N≦0.025%)すること
により靭性と溶接性が改善された。In recent years, C and N have been extremely reduced (typically C≦0.030w
t% (hereinafter simply expressed as %) (N≦0.025%), the toughness and weldability were improved.
一方、耐食性はCrとMoが高くなるほど向上し、高C
r、高Mo合金はどより厳しい環境下で用いられる。On the other hand, the corrosion resistance improves as the Cr and Mo contents increase;
r, high Mo alloys are used in harsher environments.
しかし、従来の溶鋼→インゴット→分塊→熱延→冷延の
方法で鋼板にする場合、CrとMoを増量すると特に熱
間加工において脆性が顕著になり、実質的に分塊や熱延
が不可能になる。このためにCrは30%、Moは4%
の最大添加量に限られている。However, when making a steel plate using the conventional method of molten steel → ingot → blooming → hot rolling → cold rolling, increasing the amount of Cr and Mo causes brittleness to become noticeable, especially during hot working, and in reality, blooming and hot rolling become more pronounced. becomes impossible. For this purpose, Cr is 30% and Mo is 4%.
limited to the maximum amount added.
このようにあるいはさらに高いCrないしはMoを含有
するPe −Cr −Mo系合金鋼による、高耐食性フ
ェライト系スーパーステンレス鋼ストリップの有利な製
造方法をここに提案しようとするものである。An advantageous method for producing highly corrosion-resistant ferritic super stainless steel strip using Pe--Cr--Mo alloy steel containing such or even higher Cr or Mo content is proposed herein.
(従来の技術)
平野忠男二日木材料学会 腐食防食部門委員会資料、
120.1 (1984)23には、代表的な高純度
フェライト系スーパーステンレス鋼について開示されま
た、
25Cr −4Mo −4Ni −(Ti)、26Cr
−3Mo−2,5Ni−8(Ti)、29Cr −4
Mo −2Ni。(Conventional technology) Tadao Hirano, Materials of the Futsuki Materials Society, Corrosion Prevention Division Committee,
120.1 (1984) 23 discloses typical high-purity ferritic super stainless steels, and also discloses 25Cr-4Mo-4Ni-(Ti), 26Cr
-3Mo-2,5Ni-8(Ti), 29Cr-4
Mo-2Ni.
30Cr−2Mo−0,18Ni−(Cu、 Si)、
19Cr−2Mo 0.48(T%+Nb)、26C
r−1,3Mo −0,17Ni−(Cu、 Si)及
び、26Cr −I M。30Cr-2Mo-0,18Ni-(Cu, Si),
19Cr-2Mo 0.48 (T%+Nb), 26C
r-1,3Mo-0,17Ni-(Cu, Si) and 26Cr-IM.
が商用に供されている。is available commercially.
(発明が解決しようとする問題点)
CrとMoの添加を増量すると、耐食性が向上し、より
か酷な環境において使用が可能となる点でメリットが大
きい反面製造が困難になる。(Problems to be Solved by the Invention) Increasing the addition of Cr and Mo has great advantages in that corrosion resistance improves and it can be used in harsher environments, but on the other hand, it becomes difficult to manufacture.
それというのは代表的な脆化要因として「σ脆性」があ
り、800℃付近で加熱されたときσ相というオーダー
相が形成されて脆くなるからである。This is because "σ brittleness" is a typical embrittlement factor, and when heated at around 800°C, an order phase called the σ phase is formed and becomes brittle.
従来のプロセスにおいてはインゴットを分塊、熱延する
工程で素材が熱間加工の前に、通常1000℃以上で加
熱され600〜1000℃で加工されるので、σ相の発
生が防ぎ切れずそのために、Cr 30%以上、Mo4
%以上では分塊、熱延において、割れが生じて破断し、
製造が不可能となり、かりに800℃以上で、熱延を施
せたとしても冷却時に微細なりラックが生じて、後の工
程が実質的に不可能かあるいは、良品の歩留が低下する
。In the conventional process, in the process of blooming and hot rolling the ingot, the material is usually heated to over 1000℃ and processed at 600 to 1000℃ before hot working, so the generation of σ phase cannot be prevented. , Cr 30% or more, Mo4
% or more, cracks occur and break during blooming and hot rolling,
Manufacturing becomes impossible, and even if hot rolling can be carried out at temperatures above 800° C., fine racks are generated during cooling, making subsequent processes virtually impossible or reducing the yield of good products.
そこで従来プロセスとは全く異なった製造プロセスをと
ることによって、脆性の問題点を克服し、高Cr、高M
oO高耐食性フェライト系スーパーステンレス鋼板の有
利な製造方法を提案することがこの発明の目的である。Therefore, by adopting a manufacturing process that is completely different from the conventional process, we have overcome the problem of brittleness and have achieved high Cr and high M.
It is an object of the present invention to propose an advantageous method for manufacturing oO highly corrosion resistant ferritic super stainless steel sheets.
(問題点を解決するための手段)
この発明はFe−Cr −Mo系合金溶鋼をストリップ
キャスターに供給して、直接にフェライト系ステンレス
鋼ストリップを製造するに際して、該ストリップがキャ
スターの移動冷却体から離脱して巻取られ冷却される間
に、該ストリップの温度が700〜900℃に滞留する
時間T (min)を1og T≦3−1/15〔Cr
(%)+3Mo(χ)〕の範囲に制御すること
を特徴とする高耐食性フェライト系スーパーステンレス
鋼ストリップの製造方法であり、実施態様としてFe
−Cr −Mo系合金溶鋼の組成が、C: 0.025
wt%以下、
Si : 1.0wt%以下、
Mn : 1.0wt%以下、
N : 0.025 wt%以下でかつCr : 22
.0wt%以上、Mo : 1.0wt%以上を60≧
(%)+3・Mo(χ)〕≧28の範囲で含み、残余は
Fe及び不可避的不純物より成るものであること、Fe
−Cr −Mo系合金溶鋼の組成が、
C: 0.025 wt%以下、
Si : 1.0wt%以下、
Mn : 1.O’wt%以下、
N : 0.025 wt%以下でかつCr : 22
.0wt%以上、Mo : 1.0wt%以上を60≧
(%)+3・Mo(χ)〕≧28の範囲で含み、さらに
Ti、 Nb及びZrをそれらの和で1.0 wt%以
下を含有し、残余はFe及び不可避不純物よりなるもの
であること、Fe−Cr−Mo系合金溶鋼の組成が、
C: 0.025−1%以下、
Si : 1.0wt%以下、
Mn : 1.0wt%以下、
N : 0.025 tnt%以下でかつCr : 2
2.0wt%以上と、Mo : 1.Oiyt%以上を
60≧(%)+3・Mo(χ)〕≧28の範囲で含み、
さらに4.0 wt%以下のNiと0.5 wt%以下
のCuとを含有し、残余はFe及び不可避不純物よりな
るものであること、及びPe −Cr −Mo系合金溶
鋼の組成が、
C: 0.025 wt%以下、
Si : 1.0wt%以下、
Mn : 1.Oiyt%以下、
N : 0.025 wt%以下テカッCr : 22
.0wt%以上、Mo : 1.0wt%以上を60≧
(%)+3・Mo(χ)]≧28の範囲で含み、さらに
Ti、 Nb及びZrをそれらの和で1.0wt%以下
並びに4.0wt%以下のNiと0.5 wt%以下の
Cuとを含有し、残余はFe及び不可避不純物よりなる
ものであることがそれぞれ推奨される。(Means for Solving the Problems) The present invention provides a method for directly producing ferritic stainless steel strip by supplying Fe-Cr-Mo alloy molten steel to a strip caster, in which the strip is removed from the movable cooling body of the caster. The time T (min) during which the temperature of the strip stays at 700 to 900°C while being uncoiled, coiled and cooled is 1og T≦3-1/15 [Cr
(%)+3Mo(χ)] is a method for producing a highly corrosion-resistant ferritic super stainless steel strip, and as an embodiment, Fe
-Cr-Mo alloy molten steel has a composition of C: 0.025
wt% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025 wt% or less, and Cr: 22
.. 0wt% or more, Mo: 1.0wt% or more 60≧
(%)+3・Mo(χ)] ≧28, with the remainder consisting of Fe and unavoidable impurities;
-Cr-Mo alloy molten steel has the following composition: C: 0.025 wt% or less, Si: 1.0 wt% or less, Mn: 1. O'wt% or less, N: 0.025 wt% or less, and Cr: 22
.. 0wt% or more, Mo: 1.0wt% or more 60≧
(%)+3・Mo(χ)]≧28, and further contains Ti, Nb, and Zr in a total amount of 1.0 wt% or less, with the remainder consisting of Fe and unavoidable impurities. , the composition of the Fe-Cr-Mo alloy molten steel is: C: 0.025-1% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025 tnt% or less, and Cr : 2
2.0 wt% or more, Mo: 1. Including Oiyt% or more in the range of 60≧(%)+3・Mo(χ)]≧28,
Furthermore, it contains 4.0 wt% or less of Ni and 0.5 wt% or less of Cu, with the remainder consisting of Fe and unavoidable impurities, and the composition of the Pe-Cr-Mo alloy molten steel is C : 0.025 wt% or less, Si: 1.0 wt% or less, Mn: 1. Oiyt% or less, N: 0.025 wt% or less Cr: 22
.. 0wt% or more, Mo: 1.0wt% or more 60≧
(%)+3・Mo(χ)]≧28, and further contains Ti, Nb, and Zr in a sum of 1.0 wt% or less, 4.0 wt% or less of Ni, and 0.5 wt% or less of Cu. It is recommended that the alloy contains Fe and unavoidable impurities, with the remainder consisting of Fe and unavoidable impurities.
ここにCrとMoの増量のネックは熱間脆性であるので
、分塊や熱延を省略したストリップキャスターによって
ストリップを製造し、必要に応じて、焼鈍と冷延を施し
て鋼板に仕上げれば、高Cr・高Moの鋼板が製造でき
ると考えまた実験を重ねた。The bottleneck in increasing the amount of Cr and Mo is hot brittleness, so if strips are manufactured using a strip caster that eliminates blooming and hot rolling, and if necessary, they are finished into steel sheets by annealing and cold rolling. We thought that it would be possible to produce a high Cr/high Mo steel plate and conducted repeated experiments.
第1図に示す双ロールキャスターおよび第2図に示す単
ロールキャスターによって0.2〜3.0 mm厚のス
トリップを作成した。Strips with a thickness of 0.2 to 3.0 mm were produced using a twin roll caster as shown in FIG. 1 and a single roll caster as shown in FIG.
ストリップの形成能は、Cr (!: Moを増量して
も5LIS 304の場合と比べて特に劣ることはなく
1.1’の鋳造ロールで製板され、2の冷却ゾーンでガ
スあるいは水などの冷媒により冷却され、3の巻取機で
コイルに巻取られる。The strip forming ability is not particularly inferior to that of 5LIS 304 even if the amount of Cr (!: Mo) is increased. It is cooled by a refrigerant and wound into a coil by a winding machine No. 3.
ところが高Cr、高Moの場合巻取られたコイルを次工
程のために巻き戻すと、割れが発生し、極端な時にはト
リミングすら出来ない状態であった。However, in the case of high Cr and high Mo, cracks occur when the wound coil is unwound for the next process, and in extreme cases, even trimming is not possible.
この原因は調査の結果、700〜900℃で生成する脆
いσ相の生成によるものであることが判明した。巻取り
前のストリップの冷却を強化するか又は、コイルを直ち
に水冷するなどして700〜900℃の領域を急冷する
と、靭性のあるコイルが得られることが見出されたので
ある。As a result of investigation, it was found that the cause of this was due to the formation of brittle σ phase that is generated at 700 to 900°C. It has been found that a coil with good toughness can be obtained by rapidly cooling the 700-900° C. region, such as by strengthening the cooling of the strip before winding or immediately cooling the coil with water.
(作 用)
この発明の目的とする高耐食性、特に耐すきま腐食性と
耐海水性を持たせるためには、22%以上のCrと1%
以上のMoの含有がFe −Cr −Mo系合金溶鋼組
成上の前提である。耐食性は大略、Cr+3M。(Function) In order to have high corrosion resistance, especially crevice corrosion resistance and seawater resistance as the object of this invention, 22% or more Cr and 1%
The above content of Mo is a prerequisite for the composition of Fe-Cr-Mo alloy molten steel. Corrosion resistance is approximately Cr+3M.
の量に比例するので、Cr量 3 Mo〉28%の含有
が実施上必要とされ、その一方、%)+3Mo(χ)の
量が60%を超えてももはや耐食性は顕著には向上しな
いので、原料コストや製造の困難度から60%どまりと
する。Since it is proportional to the amount of Cr content, it is practically necessary to contain Cr content of 3Mo>28%.On the other hand, even if the content of %)+3Mo(χ) exceeds 60%, the corrosion resistance will no longer improve significantly. However, it is limited to 60% due to the cost of raw materials and the difficulty of manufacturing.
MnはSなどの靭性に悪影響を及ぼす作用を殺すために
1.0%以下とする。Mn is set to 1.0% or less in order to eliminate the effects of S and other substances that adversely affect toughness.
Siは脱酸剤として好適には1.0%までとする。As a deoxidizing agent, Si is preferably contained in an amount up to 1.0%.
次に一般にフェライト系ステンレス鋼にとってC,Nは
Crを粒界にて炭・窒化させ耐粒界腐食性と靭性を悪く
させるので、低く抑えるのが好ましく、それぞれ0.0
25%とする。Next, in general, for ferritic stainless steel, C and N carbonate and nitride Cr at grain boundaries, worsening intergranular corrosion resistance and toughness, so it is preferable to keep them low, and each is 0.0
It shall be 25%.
この発明で所期する通常の用途には、以上の組成で充分
であるが、化学プラント容器などのか酷な腐食環境用途
には、Ti、 Nb及びZrを添加してさらにC,Nを
固定させCrの析出物を抑えるのが良く、C,Nがそれ
ぞれ0.025%の範囲にあってはNb+Ti+Zrの
和にて1%で充分である。The above composition is sufficient for the normal use intended for this invention, but for use in severe corrosive environments such as chemical plant containers, Ti, Nb and Zr may be added to further fix C and N. It is better to suppress Cr precipitates, and if C and N are each in the range of 0.025%, a total of 1% of Nb+Ti+Zr is sufficient.
またNi、 Cuについては、高温強度や耐食性が改善
されるので、本発明においては添加することができるが
、Ni量が高くなるとフェライト相が不安定になる上に
冷間で脆くなり、またCr量が高くなると熱間で脆くな
るため、それぞれ4%以下、0.5%以下で含有させる
。Furthermore, Ni and Cu can be added in the present invention because they improve high-temperature strength and corrosion resistance. If the amount is too high, it becomes brittle under hot conditions, so they are contained in amounts of 4% or less and 0.5% or less, respectively.
以上の組成に調整された溶鋼は、第1.2図に示される
ようなストリップキャスターによって、厚みが0.2〜
3.0 mmのストリップに直接に鋳造され、このスト
リップキャスターには第1図の双ロール法又は第2図の
単ロール法のいずれの方法を適用しても、この発明の目
的は達せられる。The molten steel adjusted to the above composition is processed by a strip caster as shown in Figure 1.2 to a thickness of 0.2~
The object of the present invention can be achieved by directly casting a 3.0 mm strip, and whether the strip caster is applied with either the twin roll method of FIG. 1 or the single roll method of FIG. 2.
なお双ロール法においては異径および傾斜双ロール法も
この発明の目的に合致する。In addition, in the twin roll method, the different diameter and inclined twin roll methods also meet the purpose of the present invention.
鋳造ロールから離脱したストリップは通常、800〜1
200℃の温度にあり、自然放冷または強制冷却によっ
て冷却した上で巻取る。The strip that leaves the casting roll typically has a thickness of 800 to 1
The material is at a temperature of 200° C., and is cooled by natural cooling or forced cooling before winding.
巻取られたコイルは強制冷却をしない場合、その巻取り
の内部温度は見掛は上少し上昇しく復熱現象)その後ゆ
っくりと下降する。If the wound coil is not forcedly cooled, the internal temperature of the wound coil will appear to rise slightly (recuperation phenomenon) and then slowly drop.
ストリップの冷却は厚みが大きい程、徐冷になることは
言うまでもないが、この発明のエツセンスはこの冷却に
ある。It goes without saying that the thicker the strip, the slower the cooling becomes, and the essence of this invention lies in this cooling.
すなわち、Crが20%以上、Moが1%以上のステン
レス鋼において、キャスティングのあと次工程としての
トリミング、酸洗、あるいは焼鈍に移るまでに、700
〜900℃の温度範囲に長時間滞留すると、ストリップ
は脆化し次工程において割れが発生して工程が困難にな
るか、又は、歩留が低下してしまうからであり、この点
に関しすでに述べた知見に基いてこの発明を完成させた
ものである。In other words, in stainless steel containing 20% or more of Cr and 1% or more of Mo, 700%
This is because if the strip remains in the temperature range of ~900°C for a long time, it will become brittle and cracks will occur in the next process, making the process difficult or reducing the yield, as already mentioned in this regard. This invention was completed based on this knowledge.
700〜900″Cの滞留時間に対して、Cr+3M。Cr+3M for residence time of 700-900″C.
(wt%)をプロットし、可撓性の良否を層別すると、
滞留時間T(min)がlog T≦3−−(Cr+3
Mo) (%1t%)の条件にあると、可撓性が良好
であることが実験的に確認され、この条件は単、双ロー
ルの別、あるいは組成の別に関係なく成立していると見
ることができる。(wt%) and stratify the quality of flexibility.
The residence time T (min) is log T≦3−−(Cr+3
It has been experimentally confirmed that the flexibility is good when the condition is Mo) (%1t%), and this condition is considered to hold regardless of whether it is a single roll, double roll, or composition. be able to.
(実施例)
表1に示す組成の溶鋼を双ロールおよび単ロール法によ
って0.2〜3.0 trm厚のストリップに直接鋳造
し、コイルに巻きとった。(Example) Molten steel having the composition shown in Table 1 was directly cast into a strip having a thickness of 0.2 to 3.0 trm by twin roll and single roll methods, and wound into a coil.
冷却ロールからコイラーまでは、光温度計によって板温
を計測した。また巻取中のコイルにPR熱電対を差し入
れてコイル内部の板温を室温に冷却するまで測定した。From the cooling roll to the coiler, the plate temperature was measured using an optical thermometer. In addition, a PR thermocouple was inserted into the coil during winding, and the plate temperature inside the coil was measured until the coil was cooled to room temperature.
冷却パターンを種々に変化させべく、コイラー前の冷却
ゾーンで、空冷や水冷を施したり、又、巻取後、直ちに
コイルを水中に浸漬した。このようにして板が900℃
から700℃に冷却される滞留時間を求めた。In order to vary the cooling pattern, air cooling or water cooling was applied in the cooling zone in front of the coiler, or the coil was immersed in water immediately after winding. In this way, the plate is heated to 900℃.
The residence time for cooling from to 700°C was determined.
コイルは次工程に渡され、酸洗あるいはグラインダーベ
ルト研削などのラインで表面入手をされたり、又は、焼
鈍ラインに付されるがこの工程において、コイルが巻き
戻される時に、可撓性を判断して良−劣の区別をした。The coil is passed on to the next process, where it is surface-obtained on a line such as pickling or grinder belt grinding, or sent through an annealing line, during which the flexibility is determined as the coil is unwound. I made a distinction between good and bad.
すなわち良は、板にクラックなどの有害な欠陥がなく、
工業的に安定して通板できる。一方、劣は板にクラック
、面折れ、割れなどが認められるか、又は巻き戻し中に
発生して、次工程への移行が工業的に不可能である。In other words, good means that the board has no harmful defects such as cracks.
Industrially stable threading is possible. On the other hand, if the board is inferior, cracks, surface folds, cracks, etc. are observed in the board, or they occur during unwinding, making it industrially impossible to proceed to the next process.
(発明の効果)
高耐食の機能をもつフェライト系ステンレス鋼板が求め
られているが、そのためのCrとMoの増量は従来工程
では限界があったのに対しこの発明では、直接製板法を
用いてしかも700〜900″Cの範囲の冷却を強化す
ることにより、CrとMoの増量が可能となり、高耐食
の板が製造できるようになった。(Effects of the invention) There is a demand for ferritic stainless steel sheets with high corrosion resistance, but there was a limit to increasing the amount of Cr and Mo in the conventional process, but this invention uses a direct sheet manufacturing method. Moreover, by strengthening the cooling in the range of 700 to 900''C, it has become possible to increase the amounts of Cr and Mo, and it has become possible to manufacture plates with high corrosion resistance.
第1図は双ロール式ストリップキャスターの模式図、
第2図は単ロール式ストリップキャスターの模式図であ
り、
第3図は可撓性に与える滞留時間とCr+3Moiの関
係を示すグラフである。FIG. 1 is a schematic diagram of a twin-roll strip caster, FIG. 2 is a schematic diagram of a single-roll strip caster, and FIG. 3 is a graph showing the relationship between residence time and Cr+3Moi on flexibility.
Claims (1)
ーに供給して、直接にフェライト系ステンレス鋼ストリ
ップを製造するに際して、 該ストリップがキャスターの移動冷却体から離脱して巻
取られ冷却される間に、該ストリップの温度が700〜
900℃に滞留する時間T(min)を logT≦3−1/15〔Cr(%)+3Mo(%)〕 の範囲に制御すること を特徴とする高耐食性フェライト系スーパーステンレス
鋼ストリップの製造方法。 2、Fe−Cr−Mo系合金溶鋼の組成が、C:0.0
25wt%以下、 Si:1.0wt%以下、 Mn:1.0wt%以下、 N:0.025wt%以下でかつ Cr:22.0wt%以上、Mo:1.0wt%以上を 60≧〔Cr(%)+3・Mo(%)〕≧28 の範囲で含み、残余はFe及び不可避的不純物より成る
ものである特許請求の範囲第1項に記載した方法。 3、Fe−Cr−Mo系合金溶鋼の組成が、C:0.0
25wt%以下、 Si:1.0wt%以下、 Mn:1.0wt%以下、 N:0.025wt%以下でかつ Cr:22.0wt%以上、Mo:1.0wt%以上を
60≧〔Cr(%)+3・Mo(%)〕≧28の範囲で
含み、さらにTi、Nb及びZrをそれらの和で1.0
wt%以下で含有し、残余はFe及び不可避不純物より
なるものである、特許請求の範囲第1項に記載した方法
。 4、Fe−Cr−Mo系合金溶鋼の組成が、C:0.0
25wt%以下、 Si:1.0wt%以下、 Mn:1.0wt%以下、 N:0.025wt%以下でかつ Cr:22.0wt%以上、Mo:1.0wt%以上を 60≧〔Cr(%)+3・Mo(%)〕≧28 の範囲で含み、さらに4.0wt%以下のNiと0.5
wt%以下のCuとを含有し、残余はFe及び不可避不
純物よりなるものである、特許請求の範囲第1項に記載
した方法。 5、Fe−Cr−Mo系合金溶鋼の組成が、C:0.0
25wt%以下、 Si:1.0wt%以下、 Mn:1.0wt%以下、 N:0.025wt%以下でかつ Cr:22.0wt%以上、Mo:1.0wt%以上を 60≧〔Cr(%)+3・Mo(%)〕≧28 の範囲で含み、 さらにTi、Nb及びZrをそれらの和で1.0wt%
以下 並びに4.0wt%以下のNiと0.5wt%以下のC
uとを含有し、残余はFe及び不可避不純物よりなるも
のである、特許請求の範囲第1項に記載した方法。[Claims] 1. When Fe-Cr-Mo alloy molten steel is supplied to a strip caster to directly produce a ferritic stainless steel strip, the strip is separated from the movable cooling body of the caster and wound up. While the strip is being cooled, the temperature of the strip is between 700 and 700℃.
A method for producing a highly corrosion-resistant ferritic super stainless steel strip, which comprises controlling the residence time T (min) at 900°C within the range of logT≦3-1/15 [Cr (%) + 3Mo (%)]. 2. The composition of the Fe-Cr-Mo alloy molten steel is C: 0.0
25wt% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025wt% or less, and Cr: 22.0wt% or more, Mo: 1.0wt% or more with 60≧[Cr( %)+3.Mo(%)]≧28, with the remainder consisting of Fe and unavoidable impurities. 3. The composition of the Fe-Cr-Mo alloy molten steel is C: 0.0
25wt% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025wt% or less, and Cr: 22.0wt% or more, Mo: 1.0wt% or more with 60≧[Cr( %)+3・Mo(%)] in the range of ≧28, and further contains Ti, Nb, and Zr with a sum of 1.0
The method according to claim 1, wherein the content is less than or equal to wt%, with the remainder consisting of Fe and unavoidable impurities. 4. The composition of the Fe-Cr-Mo alloy molten steel is C: 0.0
25wt% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025wt% or less, and Cr: 22.0wt% or more, Mo: 1.0wt% or more with 60≧[Cr( %) + 3・Mo(%)] ≧ 28, and further contains 4.0 wt% or less of Ni and 0.5
2. The method according to claim 1, wherein the copper content is less than or equal to wt% of Cu, with the remainder consisting of Fe and unavoidable impurities. 5. The composition of the Fe-Cr-Mo alloy molten steel is C: 0.0
25wt% or less, Si: 1.0wt% or less, Mn: 1.0wt% or less, N: 0.025wt% or less, and Cr: 22.0wt% or more, Mo: 1.0wt% or more with 60≧[Cr( %)+3・Mo(%)]≧28, and further contains Ti, Nb, and Zr in a sum of 1.0wt%.
and below and 4.0wt% or less Ni and 0.5wt% or less C
2. The method according to claim 1, which contains u and the remainder consists of Fe and unavoidable impurities.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP31518687A JPH01157743A (en) | 1987-12-15 | 1987-12-15 | Production of high corrosion resistant ferritic super stainless steel strip |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP31518687A JPH01157743A (en) | 1987-12-15 | 1987-12-15 | Production of high corrosion resistant ferritic super stainless steel strip |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH01157743A true JPH01157743A (en) | 1989-06-21 |
JPH0433538B2 JPH0433538B2 (en) | 1992-06-03 |
Family
ID=18062455
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP31518687A Granted JPH01157743A (en) | 1987-12-15 | 1987-12-15 | Production of high corrosion resistant ferritic super stainless steel strip |
Country Status (1)
Country | Link |
---|---|
JP (1) | JPH01157743A (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1058528C (en) * | 1995-04-14 | 2000-11-15 | 新日本制铁株式会社 | Equipment for manufacturing stainless steel strip |
Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6056767A (en) * | 1983-09-07 | 1985-04-02 | Ricoh Co Ltd | Arranging mechanism for discharged paper |
-
1987
- 1987-12-15 JP JP31518687A patent/JPH01157743A/en active Granted
Patent Citations (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS6056767A (en) * | 1983-09-07 | 1985-04-02 | Ricoh Co Ltd | Arranging mechanism for discharged paper |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
CN1058528C (en) * | 1995-04-14 | 2000-11-15 | 新日本制铁株式会社 | Equipment for manufacturing stainless steel strip |
Also Published As
Publication number | Publication date |
---|---|
JPH0433538B2 (en) | 1992-06-03 |
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