JP2015078415A - HIGH-Al-CONTAINING FERRITIC STAINLESS STEEL SHEET AND PRODUCTION METHOD THEREOF, AND HIGH-Al-CONTAINING FERRITIC STAINLESS FOIL - Google Patents
HIGH-Al-CONTAINING FERRITIC STAINLESS STEEL SHEET AND PRODUCTION METHOD THEREOF, AND HIGH-Al-CONTAINING FERRITIC STAINLESS FOIL Download PDFInfo
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- 229910001220 stainless steel Inorganic materials 0.000 title claims abstract description 57
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 26
- 239000011888 foil Substances 0.000 title claims abstract description 12
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 78
- 239000010959 steel Substances 0.000 claims abstract description 78
- 230000007547 defect Effects 0.000 claims abstract description 33
- 238000005096 rolling process Methods 0.000 claims abstract description 29
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 16
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 11
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 4
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 3
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims description 29
- 238000001816 cooling Methods 0.000 claims description 23
- 229910052750 molybdenum Inorganic materials 0.000 claims description 23
- 238000005098 hot rolling Methods 0.000 claims description 22
- 229910052721 tungsten Inorganic materials 0.000 claims description 22
- 239000000203 mixture Substances 0.000 claims description 16
- 238000005097 cold rolling Methods 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 5
- 229910052698 phosphorus Inorganic materials 0.000 claims description 2
- 229910052717 sulfur Inorganic materials 0.000 claims description 2
- 238000005336 cracking Methods 0.000 description 21
- 238000000034 method Methods 0.000 description 18
- 230000000694 effects Effects 0.000 description 14
- 230000003647 oxidation Effects 0.000 description 14
- 238000007254 oxidation reaction Methods 0.000 description 14
- 239000010960 cold rolled steel Substances 0.000 description 11
- 230000007797 corrosion Effects 0.000 description 10
- 238000005260 corrosion Methods 0.000 description 10
- 230000007423 decrease Effects 0.000 description 10
- 229910052761 rare earth metal Inorganic materials 0.000 description 10
- 230000008646 thermal stress Effects 0.000 description 9
- 239000010935 stainless steel Substances 0.000 description 7
- 238000011156 evaluation Methods 0.000 description 5
- 230000007704 transition Effects 0.000 description 5
- 238000007670 refining Methods 0.000 description 4
- 241000264877 Hippospongia communis Species 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 2
- KRHYYFGTRYWZRS-UHFFFAOYSA-N Fluorane Chemical compound F KRHYYFGTRYWZRS-UHFFFAOYSA-N 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- 239000003054 catalyst Substances 0.000 description 2
- 230000001276 controlling effect Effects 0.000 description 2
- 230000002950 deficient Effects 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000009966 trimming Methods 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910052779 Neodymium Inorganic materials 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 229910052777 Praseodymium Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 229910001566 austenite Inorganic materials 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005422 blasting Methods 0.000 description 1
- 239000000969 carrier Substances 0.000 description 1
- 238000002485 combustion reaction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000002596 correlated effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 238000009413 insulation Methods 0.000 description 1
- 229910052747 lanthanoid Inorganic materials 0.000 description 1
- 150000002602 lanthanoids Chemical class 0.000 description 1
- 229910052746 lanthanum Inorganic materials 0.000 description 1
- 238000012423 maintenance Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 238000003303 reheating Methods 0.000 description 1
- 229910052706 scandium Inorganic materials 0.000 description 1
- 238000002791 soaking Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000002436 steel type Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 229910052727 yttrium Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、高Al含有フェライト系ステンレス鋼板およびその製造方法ならびに高Al含有フェライト系ステンレス箔に関する。 The present invention relates to a high Al content ferritic stainless steel sheet, a method for producing the same, and a high Al content ferritic stainless steel foil.
Alを2.5質量％以上含有する高Al含有フェライト系ステンレス鋼板は、高温での耐酸化性に優れるため、ステンレス箔に加工され、自動車、オートバイ、マリンバイク、モーターボート、大型芝刈り機、小型発電機などの排ガス浄化装置用触媒担体（メタルハニカム）に使用されている。また、薄板の形状でストーブや加熱炉の部材、ヒーターの発熱体などに使用されている。 High Al content ferritic stainless steel sheets containing 2.5% by mass or more of Al have excellent oxidation resistance at high temperatures, so they are processed into stainless steel foils. It is used as a catalyst carrier (metal honeycomb) for exhaust gas purification devices such as. Moreover, it is used in the shape of a thin plate as a heater, a heating furnace member, a heater heating element, or the like.
一方、高Al含有フェライト系ステンレス鋼板は製造性が悪く、表面疵や割れなどの欠陥が生じやすいという問題を抱えている。この要因の一つとして、鋳造スラブやインゴットに生じる割れが挙げられる。高Al含有フェライト系ステンレス鋼は鋳造組織が脆く、スラブもしくはインゴットの冷却中や、表面手入れ中、あるいは熱間圧延前の加熱中などに割れを生じやすい。スラブやインゴットに発生した割れは、その後熱間圧延や冷間圧延を行っても表面欠陥や内部欠陥として残存し、除去工程の負荷増大や歩留まりを大幅に低下させる。スラブ割れによって生じる熱延鋼板や冷延鋼板の欠陥は、高Al含有フェライト系ステンレス鋼板製造工程における大きな問題となっている。 On the other hand, a high Al content ferritic stainless steel sheet has a problem in that the manufacturability is poor and defects such as surface flaws and cracks are likely to occur. One of the factors is a crack that occurs in a cast slab or ingot. High Al-containing ferritic stainless steel has a brittle cast structure and is prone to cracking during cooling of the slab or ingot, surface maintenance, or heating before hot rolling. Cracks generated in slabs and ingots remain as surface defects or internal defects even if hot rolling or cold rolling is performed thereafter, which greatly increases the load and yield of the removal process. Defects in hot-rolled steel sheets and cold-rolled steel sheets caused by slab cracking are a major problem in the production process of high Al-containing ferritic stainless steel sheets.
スラブ割れが生じる要因の一つとして、冷却中スラブの内部温度偏差に起因して生じる熱応力が挙げられる。鋳造後のスラブを冷却すると、ある温度で熱応力がスラブの破断応力を上回り、その結果割れが発生するという考え方である。つまり、スラブ割れを防止し欠陥の少ない圧延鋼板を安定して製造するためには、スラブ冷却中の熱応力を緩和すること、スラブが割れ発生温度を下回る前に熱間圧延加熱炉に装入して昇温することが重要となる。 One of the factors that cause slab cracking is thermal stress caused by the internal temperature deviation of the slab during cooling. The idea is that when the slab after casting is cooled, the thermal stress exceeds the breaking stress of the slab at a certain temperature, resulting in cracks. In other words, in order to prevent slab cracking and stably produce rolled steel sheets with few defects, it is necessary to relieve thermal stress during slab cooling, and to insert into a hot rolling heating furnace before the slab falls below the cracking temperature. It is important to raise the temperature.
これらの知見に基づき、例えば、特許文献1には、Mo、Zr、Nbのうち1種以上を含有するフェライト系ステンレス鋼スラブを150℃以下に冷却することなく加熱して熱間圧延する方法が開示されている。 Based on these findings, for example, Patent Document 1 discloses a method of heating and hot rolling a ferritic stainless steel slab containing at least one of Mo, Zr, and Nb without cooling to 150 ° C. or less. It is disclosed.
特許文献2には、スラブ自身の延性−脆性遷移温度以下に冷却しないまま熱延加熱炉に再装入することで割れを抑制する方法が開示されている。 Patent Document 2 discloses a method of suppressing cracking by re-inserting into a hot-rolling heating furnace without cooling below the ductile-brittle transition temperature of the slab itself.
特許文献3には、TiSとTiCの総量を規定し、さらにスラブ中央部と表面の温度偏差が200℃以下となるよう制御することで、スラブを常温まで冷却可能とする方法が開示されている。 Patent Document 3 discloses a method that allows the slab to be cooled to room temperature by defining the total amount of TiS and TiC and further controlling the temperature deviation between the center of the slab and the surface to be 200 ° C. or less. .
近年、自動車の燃費向上を目的に排ガス温度は上昇する傾向にあり、触媒担体に用いられるメタルハニカム用高Al含有フェライト系ステンレス鋼箔には、さらに優れた耐酸化性および高温強度が求められている。そのため、Cr含有量を高めたり、Mo、W、REMなどの合金元素を添加した高Al含有フェライト系ステンレス鋼板が開発されている。しかし、これらの合金元素の添加は、スラブの割れ感受性を増大させる。例えば、Cr含有量の増加およびMo、Wの添加は、フェライト系ステンレス鋼板特有の脆化現象である475℃脆性や金属間化合物相の析出を促進させる。これらの現象が生じると、破断応力が低下しより低い熱応力でも破断しやすくなる。さらには、延性−脆性遷移温度も上昇し、より高い温度で割れが発生する可能性が高まる。また、REMは粒界に脆化相として析出してスラブ割れの起点となるため、添加されるとスラブ割れ感受性を増大させる。このように、Cr、 Mo、 W、 REMの添加は、そもそもスラブ割れの生じやすい高Al含有フェライト系ステンレス鋼板のスラブ靭性をよりいっそう低下させ、割れの防止を困難にする。 In recent years, exhaust gas temperature has been increasing for the purpose of improving the fuel efficiency of automobiles, and high Al content ferritic stainless steel foils for metal honeycombs used for catalyst carriers are required to have better oxidation resistance and high temperature strength. Yes. For this reason, high Al content ferritic stainless steel sheets are being developed in which the Cr content is increased or alloy elements such as Mo, W, and REM are added. However, the addition of these alloy elements increases the slab cracking sensitivity. For example, an increase in Cr content and addition of Mo and W promote brittleness at 475 ° C. and precipitation of intermetallic compound phases, which are embrittlement phenomena unique to ferritic stainless steel sheets. When these phenomena occur, the rupture stress is reduced, and the rupture is likely to occur even at a lower thermal stress. Furthermore, the ductile-brittle transition temperature is also increased, and the possibility of cracking at a higher temperature is increased. Moreover, since REM precipitates as a brittle phase at the grain boundary and becomes the starting point of slab cracking, when added, it increases slab cracking sensitivity. Thus, the addition of Cr, Mo, W, and REM further reduces the slab toughness of the high Al-containing ferritic stainless steel sheet, which is prone to slab cracking, making it difficult to prevent cracking.
従って、特許文献1に記載の方法を適用しても、成分によっては150℃以上で割れが発生する場合があり完全に割れを防止することができない。特許文献2に記載の方法を用いても、Al、REMを含有する鋼種の場合は脆化が著しいため、遷移温度に達する以前に破断が生じる場合があり全ての割れを防ぐことはできない。さらに、特許文献2では、徐冷した鋳片より採取した試験片を用いて延性−脆性遷移温度を測定しているが、高Al含有フェライト系ステンレス鋼板では、室温まで鋳片を冷却するとほとんどの場合内部に割れが発生してしまう。このため、健全な試験片を採取することができず延性−脆性遷移温度の測定が困難である。特許文献3に記載の方法のように温度偏差を200℃以内に制御して熱応力の緩和を試みても、高Al含有フェライト系ステンレス鋼板は脆化が著しいためわずかな熱応力で破断に至り室温までの冷却は困難である。また、以上の問題は、高温強度の向上を目的にMoやWを添加した場合により顕著になる。 Therefore, even if the method described in Patent Document 1 is applied, cracks may occur at 150 ° C. or higher depending on the components, and cannot be completely prevented. Even if the method described in Patent Document 2 is used, in the case of a steel type containing Al and REM, since embrittlement is significant, fracture may occur before the transition temperature is reached, and all cracks cannot be prevented. Furthermore, in Patent Document 2, the ductile-brittle transition temperature is measured using a test piece taken from a slowly cooled slab, but in a high Al-containing ferritic stainless steel sheet, most of the slab is cooled to room temperature. In some cases, cracks occur inside. For this reason, a healthy test piece cannot be collected and it is difficult to measure the ductile-brittle transition temperature. Even if the temperature deviation is controlled within 200 ° C as in the method described in Patent Document 3, the high Al-containing ferritic stainless steel sheet is brittle, so it breaks with a slight thermal stress. Cooling to room temperature is difficult. The above problem becomes more prominent when Mo or W is added for the purpose of improving the high-temperature strength.
本発明は、かかる事情に鑑みてなされたものであって、表面性状に優れた高Al含有フェライト系ステンレス鋼板およびその製造方法ならびに高Al含有フェライト系ステンレス箔を提供することを目的とする。 This invention is made | formed in view of this situation, Comprising: It aims at providing the high Al content ferritic stainless steel plate excellent in surface property, its manufacturing method, and a high Al content ferritic stainless steel foil.
本発明者らは上記問題を解決すべく鋭意検討した。その結果、スラブの割れを防止できるスラブの冷却可能限界温度の存在を見出した。さらに、この冷却可能限界温度はCr、Al、Mo、Wの含有量と相関性があることが明らかとなった。 The present inventors diligently studied to solve the above problems. As a result, it was found that there is a slab cooling limit temperature that can prevent cracking of the slab. Furthermore, it became clear that this coolable limit temperature is correlated with the contents of Cr, Al, Mo and W.
本発明は、以上の知見に基づきなされたものであり、その要旨は以下の通りである。
[1] 成分組成として、質量%で、C:0.001〜0.050%、Si:0.01〜2.0%、Mn:0.01〜1.0%、S:0.01%以下、P:0.05%以下、Cr:15.0〜30.0%、Ni:0.01〜0.60%、Al:2.5〜6.5%、N:0.001〜0.050%を含有し、さらに、Ti:0.01〜0.30%、Nb:0.01〜0.30%、Zr:0.005〜0.20%、Hf:0.005〜0.20%、REM:0.005〜0.20%のうちの1種以上を含有し、残部がFeおよび不可避的不純物からなり、
鋼板圧延方向端部には、長さが20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下であることを特徴とする高Al含有フェライト系ステンレス鋼板。
［2］前記［1］において、成分組成として、更に、質量%で、MoおよびWのうち少なくとも一種を合計で0.10〜6.0%含有することを特徴とする高Al含有フェライト系ステンレス鋼板。
［3］前記［1］または［2］において、成分組成として、更に、質量％で、Ca:0.0005〜0.0200％、Mg:0.0002〜0.0200％のうち少なくとも1種を含有することを特徴とする高Al含有フェライト系ステンレス鋼板。
［4］前記［1］〜［3］のいずれか一項に記載の高Al含有フェライト系ステンレス鋼板を用いた高Al含有フェライト系ステンレス箔。
［5］前記［1］に記載の成分組成からなる鋼を、スラブもしくはインゴットに鋳造し、
スラブに鋳造した場合は、スラブの表面温度が式（1）のT1℃を下回る前に加熱炉に前記スラブを装入して加熱し、次いで熱間圧延する、インゴットに鋳造した場合は、インゴットの表面温度が式（1）のT1℃を下回る前に加熱炉に前記インゴットを装入して加熱し、次いで分塊圧延し熱間圧延することを特徴とする、鋼板圧延方向端部には、20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下である高Al含有フェライト系ステンレス鋼板の製造方法。
T1=4.5Cr％＋17Al％−50 式（1）
ただし、Cr％およびAl％は、それぞれCrあるいはAlの含有量(質量%)を表す。
［6］前記［2］に記載の成分組成からなる鋼を、スラブもしくはインゴットに鋳造し、スラブに鋳造した場合は、スラブの表面温度が式（２）のT2℃を下回る前に加熱炉に前記スラブを装入して加熱し、次いで熱間圧延するインゴットに鋳造した場合は、インゴットの表面温度が式（２）のT2℃を下回る前に加熱炉に前記インゴットを装入して加熱し、次いで分塊圧延し熱間圧延することを特徴とする、鋼板圧延方向端部には、長さが20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下である高Al含有フェライト系ステンレス鋼板の製造方法。
T2=4.5Cr％＋17Al％＋6(Mo％＋W％)−50 式（2）
ただし、Cr％、Al％、Mo％およびW％は、それぞれCr、Al、Mo、Wの含有量(質量%)を表す。
［7］前記［5］または［6］において、成分組成として、更に、質量％で、Ca:0.0005〜0.0200％、Mg:0.0002〜0.0200％のうち少なくとも1種を含有することを特徴とする高Al含有フェライト系ステンレス鋼板の製造方法。
［8］前記［5］〜［7］のいずれかにおいて、加熱炉挿入前の前記スラブあるいは前記インゴットに対して、500℃〜T0℃の温度域を平均冷却速度：50℃/h以下で冷却することを特徴とする高Al含有フェライト系ステンレス鋼板の製造方法。
ただし、前記T0℃は、加熱炉挿入前のスラブ表面あるいはインゴット表面の最低温度である。
［9］前記［5］〜［8］のいずれかにおいて、前記熱間圧延後または前記分塊圧延後に、さらに冷間圧延を行うことを特徴とする高Al含有フェライト系ステンレス鋼板の製造方法。
The present invention has been made based on the above findings, and the gist thereof is as follows.
[1] As component composition, by mass, C: 0.001 to 0.050%, Si: 0.01 to 2.0%, Mn: 0.01 to 1.0%, S: 0.01% or less, P: 0.05% or less, Cr: 15.0 to 30.0% Ni: 0.01-0.60%, Al: 2.5-6.5%, N: 0.001-0.050%, Ti: 0.01-0.30%, Nb: 0.01-0.30%, Zr: 0.005-0.20%, Hf: 0.005 to 0.20%, REM: containing one or more of 0.005 to 0.20%, the balance consists of Fe and inevitable impurities,
At the end in the rolling direction of the steel sheet, the number of end cracks having a length of 20 mm or more is 1 or less per 1 m of end length, and the length in the rolling direction is 30 mm or more in the thickness direction of the steel sheet. A high Al-containing ferritic stainless steel sheet characterized in that the number of surface defects having a length of 0.1 mm or more is 5 / m 2 or less.
[2] The high Al-containing ferritic stainless steel sheet according to [1], wherein the composition further includes 0.10 to 6.0% in total of at least one of Mo and W as a component composition.
[3] In the above [1] or [2], the component composition further contains at least one of Ca: 0.0005 to 0.0200% and Mg: 0.0002 to 0.0200% by mass%. Al-containing ferritic stainless steel sheet.
[4] A high Al content ferritic stainless steel foil using the high Al content ferritic stainless steel sheet according to any one of [1] to [3].
[5] A steel having the composition described in [1] is cast into a slab or ingot,
When cast into a slab, when the slab is cast into an ingot, the surface temperature of the slab falls below T 1 ° C of the formula (1), and the slab is charged and heated, and then hot-rolled. An ingot in the rolling direction of the steel sheet, characterized in that the ingot is charged and heated in a heating furnace before the surface temperature of the ingot falls below T 1 ° C. in the formula (1), and then is rolled in pieces and hot rolled. The number of edge cracks of 20 mm or more is 1 or less per 1 m of end length, and the steel plate surface has a length in the rolling direction of 30 mm or more and a length of 0.1 mm or more in the thickness direction. A method for producing a high Al-containing ferritic stainless steel sheet having surface defects of 5 pieces / m 2 or less.
T 1 = 4.5Cr% + 17Al% -50 Formula (1)
However, Cr% and Al% represent Cr or Al content (mass%), respectively.
[6] When the steel having the composition described in [2] is cast into a slab or ingot and cast into the slab, the heating furnace is used before the surface temperature of the slab falls below T 2 ° C in the formula (2). In the case of casting into an ingot to be hot-rolled, and then hot rolling, the ingot is charged into a heating furnace before the surface temperature of the ingot falls below T 2 ° C of the formula (2). The steel plate surface is characterized in that it is heated, then split-rolled and hot-rolled, and the end portion in the steel plate rolling direction has no more than 20 mm of end cracks per 1 m of end length. The method for producing a high Al-containing ferritic stainless steel sheet having a surface defect of 5 pieces / m 2 or less having a length in the rolling direction of 30 mm or more and a length of 0.1 mm or more in the thickness direction.
T 2 = 4.5Cr% + 17Al% + 6 (Mo% + W%) − 50 Formula (2)
However, Cr%, Al%, Mo%, and W% represent the contents (mass%) of Cr, Al, Mo, and W, respectively.
[7] In the above [5] or [6], the composition further comprises at least one of Ca: 0.0005 to 0.0200% and Mg: 0.0002 to 0.0200% by mass% as a component composition. Manufacturing method of Al-containing ferritic stainless steel sheet.
[8] In any one of the above [5] to [7], the temperature range of 500 ° C. to T 0 ° C is an average cooling rate of 50 ° C./h or less with respect to the slab or the ingot before inserting the heating furnace. A method for producing a high Al content ferritic stainless steel sheet, characterized by cooling.
However, T 0 ° C. is the minimum temperature of the slab surface or ingot surface before inserting the heating furnace.
[9] The method for producing a high Al-containing ferritic stainless steel sheet according to any one of [5] to [8], wherein cold rolling is further performed after the hot rolling or the partial rolling.
なお、本発明において、高Al含有フェライト系ステンレス鋼板とは、Alを2.5％以上含有するフェライト系ステンレス鋼板であり、高Al含有フェライト系ステンレス熱延鋼板、高Al含有フェライト系ステンレス冷延鋼板のいずれも対象である。また、本明細書において、鋼の成分を示す%はすべて質量%である。 In the present invention, the high Al content ferritic stainless steel sheet is a ferritic stainless steel sheet containing 2.5% or more of Al, and is a high Al content ferritic stainless hot rolled steel sheet or a high Al content ferritic stainless steel cold rolled steel sheet. Both are subjects. Further, in the present specification, “%” indicating the components of steel is all “% by mass”.
本発明によれば、表面性状に優れた高Al含有フェライト系ステンレス鋼板、高Al含有フェライト系ステンレス箔が得られる。そして、製造工程におけるスラブ割れトラブルを著しく低減させ、表面性状に優れた高Al含有フェライト系ステンレス鋼板を安定的に得ることが可能となる。 According to the present invention, a high Al content ferritic stainless steel sheet and a high Al content ferritic stainless steel foil excellent in surface properties can be obtained. And it becomes possible to reduce slab crack trouble in a manufacturing process remarkably, and to obtain the high Al content ferritic stainless steel plate excellent in surface properties stably.
以下、本発明について詳細に説明する。 Hereinafter, the present invention will be described in detail.
(1)化学成分
C:0.001〜0.050%
C量が0.050%を超えると、スラブ靭性が低下して製造性が低下する。一方、0.001%未満にしようとすると精錬が困難になる。そのため、C量は0.001〜0.050％の範囲とする。好ましくは0.003〜0.020％の範囲である。より好ましくは0.005〜0.015％の範囲である。
(1) Chemical composition
C: 0.001 ~ 0.050%
If the amount of C exceeds 0.050%, the slab toughness decreases and the productivity decreases. On the other hand, refining becomes difficult if it is made less than 0.001%. Therefore, the C content is in the range of 0.001 to 0.050%. Preferably it is 0.003 to 0.020% of range. More preferably, it is 0.005 to 0.015% of range.
Si:0.01〜2.0%
Siは耐酸化性を向上させるが、その量が2.0%を超えると、スラブの靭性が低下して製造が困難になる。一方、0.01％未満にしようとすると精錬が困難になる。そのため、Si量は0.01〜2.0％の範囲とする。好ましくは0.05〜1.0％の範囲である。より好ましくは0.10〜0.20％の範囲である。
Si: 0.01-2.0%
Si improves the oxidation resistance, but if the amount exceeds 2.0%, the toughness of the slab is lowered and the production becomes difficult. On the other hand, refining becomes difficult if it is made less than 0.01%. Therefore, the Si content is in the range of 0.01 to 2.0%. Preferably it is 0.05 to 1.0% of range. More preferably, it is 0.10 to 0.20% of range.
Mn:0.01〜1.0%
Mn量が1.0%を超えると、鋼板の耐食性が低下する。一方、0.01％未満にしようとすると精錬が困難になる。そのため、Mn量は0.01〜1.0％の範囲とする。好ましくは0.05〜0.40％の範囲である。
Mn: 0.01-1.0%
When the amount of Mn exceeds 1.0%, the corrosion resistance of the steel sheet decreases. On the other hand, refining becomes difficult if it is made less than 0.01%. Therefore, the Mn content is in the range of 0.01 to 1.0%. Preferably it is 0.05 to 0.40% of range.
S:0.01%以下
S量が0.01%を超えると、鋼板の耐食性が低下する。よって、S量は0.01%以下、好ましくは0.005%以下、より好ましくは0.003%以下とする。
S: 0.01% or less
When the amount of S exceeds 0.01%, the corrosion resistance of the steel sheet decreases. Therefore, the S content is 0.01% or less, preferably 0.005% or less, more preferably 0.003% or less.
P:0.05%以下
P量が0.05%を超えると、鋼板の耐食性が低下する。よって、P量は0.05%以下、好ましくは0.03%以下とする。
P: 0.05% or less
When the amount of P exceeds 0.05%, the corrosion resistance of the steel sheet decreases. Therefore, the P content is 0.05% or less, preferably 0.03% or less.
Cr:15.0〜30.0%
Crは鋼板の耐食性および高温での強度および耐酸化性を確保する目的で15.0%以上含有する。しかし、Cr量が30.0%を超えると、金属間化合物の析出および475℃脆性が促進されるため靭性が著しく低下し、本発明の技術を用いてもスラブ割れの抑制が困難となる。よって、Cr量は15.0〜30.0%の範囲とする。好ましくは18.0〜28.0%の範囲である。より好ましくは、18.0〜25.0%の範囲である。
Cr: 15.0-30.0%
Cr is contained in an amount of 15.0% or more for the purpose of ensuring the corrosion resistance of the steel sheet and the strength and oxidation resistance at high temperatures. However, if the Cr content exceeds 30.0%, precipitation of intermetallic compounds and brittleness at 475 ° C. are promoted, so that the toughness is remarkably reduced, and it is difficult to suppress slab cracking even using the technique of the present invention. Therefore, the Cr content is in the range of 15.0 to 30.0%. Preferably it is 18.0 to 28.0% of range. More preferably, it is 18.0 to 25.0% of range.
Ni:0.01〜0.60%
Niは鋼板の耐食性を向上させる効果がある。その効果は、0.01%以上の含有で得られる。しかし、オーステナイト生成元素であるため、含有量が0.60%を超えると鋼板を高温で使用した際に熱膨張率の大きいオーステナイト相が生成し熱疲労特性や形状安定性の低下につながる。したがって、Ni量は0.01〜0.60%の範囲とする。好ましくは0.05〜0.20%の範囲である。
Ni: 0.01-0.60%
Ni has the effect of improving the corrosion resistance of the steel sheet. The effect is obtained when the content is 0.01% or more. However, since it is an austenite-generating element, if the content exceeds 0.60%, an austenite phase having a high coefficient of thermal expansion is generated when the steel sheet is used at a high temperature, leading to a decrease in thermal fatigue characteristics and shape stability. Therefore, the Ni content is in the range of 0.01 to 0.60%. Preferably it is 0.05 to 0.20% of range.
Al:2.5〜6.5%
Alは高温酸化時にAl2O3を主成分とする酸化皮膜を生成させて耐酸化性を向上させる元素である。Al量が2.5%以上でその効果が得られる。一方、Al量が6.5%を超えると、スラブの靭性が著しく低下し、本発明の方法を用いても割れを防ぐことが困難となる。このためAl量は2.5〜6.5%の範囲とする。好ましくは3.0〜6.0%の範囲である。
Al: 2.5-6.5%
Al is an element that improves the oxidation resistance by generating an oxide film composed mainly of Al 2 O 3 during high-temperature oxidation. The effect is obtained when the Al content is 2.5% or more. On the other hand, when the Al content exceeds 6.5%, the toughness of the slab is remarkably lowered, and it is difficult to prevent cracking even if the method of the present invention is used. For this reason, the amount of Al is made 2.5 to 6.5%. Preferably it is 3.0 to 6.0% of range.
N:0.001〜0.050%
N量が0.050%を超えると、靱性が低下するとともに、加工性の低下により製造が困難になる。一方、0.001%未満にしようとすると精錬が困難になる。よって、Ｎ量は0.001〜0.050%の範囲とする。好ましくは0.003〜0.020％の範囲である。より好ましくは0.005〜0.015％の範囲である。
N: 0.001 to 0.050%
If the N content exceeds 0.050%, the toughness decreases and the manufacturing becomes difficult due to the decrease in workability. On the other hand, refining becomes difficult if it is made less than 0.001%. Therefore, the N amount is in the range of 0.001 to 0.050%. Preferably it is 0.003 to 0.020% of range. More preferably, it is 0.005 to 0.015% of range.
Ti:0.01〜0.30%、Nb:0.01〜0.30%、Zr:0.005〜0.20%、Hf:0.005〜0.20%、REM:0.005〜0.20%のうちの1種以上
Ti:0.01〜0.30%
Tiは鋼中のCやNと結合し、スラブの靭性を向上させる効果がある。また、鋼板の耐食性や高温での耐酸化性を向上させる。これらの効果は0.01％以上の含有で得られる。しかし、0.30%を超えると、スラブの靭性を低下させる。よって、Ti量は0.01〜0.30%の範囲とする。好ましくは0.05〜0.20%の範囲である。
One or more of Ti: 0.01-0.30%, Nb: 0.01-0.30%, Zr: 0.005-0.20%, Hf: 0.005-0.20%, REM: 0.005-0.20%
Ti: 0.01 ~ 0.30%
Ti combines with C and N in the steel and has the effect of improving the toughness of the slab. It also improves the corrosion resistance of the steel sheet and the oxidation resistance at high temperatures. These effects can be obtained with a content of 0.01% or more. However, if it exceeds 0.30%, the toughness of the slab is lowered. Therefore, the Ti content is in the range of 0.01 to 0.30%. Preferably it is 0.05 to 0.20% of range.
Nb:0.01〜0.30%
Nbは鋼板の高温での強度を向上させる。この効果は0.01%以上の含有で得られる。一方、Nb量が0.30%を超えると、スラブの靭性が低下してスラブ割れが助長される。また高温での耐酸化性が著しく低下する。よって、Nb量は0.01〜0.30%の範囲とする。好ましくは0.01〜0.10%の範囲である。
Nb: 0.01-0.30%
Nb improves the strength of the steel sheet at high temperatures. This effect is obtained when the content is 0.01% or more. On the other hand, when the Nb content exceeds 0.30%, the toughness of the slab is lowered and slab cracking is promoted. Also, the oxidation resistance at high temperatures is significantly reduced. Therefore, the Nb content is in the range of 0.01 to 0.30%. Preferably it is 0.01 to 0.10% of range.
Zr:0.005〜0.20%
Zrは鋼中のCやNと結合し、スラブの靭性を向上させる効果がある。また、高温での耐酸化性を向上させる。これらの効果は0.005％以上の添加で得られる。しかし、0.20%を超えると、スラブの靭性を低下させる。よって、Zr量は0.005〜0.20%の範囲とする。好ましくは0.02〜0.08%の範囲である。
Zr: 0.005-0.20%
Zr combines with C and N in steel and has the effect of improving the toughness of the slab. It also improves oxidation resistance at high temperatures. These effects can be obtained by adding 0.005% or more. However, if it exceeds 0.20%, the toughness of the slab is lowered. Therefore, the Zr content is set to a range of 0.005 to 0.20%. Preferably it is 0.02 to 0.08% of range.
Hf:0.005〜0.20%
Hfは、高温での耐酸化性を向上させる。その効果は0.005％以上の添加で得られる。しかし、0.20%を超えると、Feなどと金属間化合物をつくりスラブの靭性が低下する。よって、Hf量は0.005〜0.20%の範囲とする。好ましくは0.02〜0.10%の範囲である。
Hf: 0.005-0.20%
Hf improves oxidation resistance at high temperatures. The effect is obtained by adding 0.005% or more. However, if it exceeds 0.20%, an intermetallic compound such as Fe is produced, and the toughness of the slab decreases. Therefore, the Hf amount is in the range of 0.005 to 0.20%. Preferably it is 0.02 to 0.10% of range.
REM:0.005〜0.20%
REMとは、Sc、Yおよびランタノイド系元素(La、Ce、Pr、Nd、Smなど原子番号57〜71までの元素)をいう。REMは高温で生成するAl2O3酸化皮膜の密着性を良好にするとともにその生成速度を低下させて耐酸化性を向上させる。これらの効果は、0.005％以上の添加で得られる。一方、0.20%を超えると、スラブの粒界に析出して破断の起点になる。よって、REM量は0.005〜0.20%の範囲とする。好ましくは0.03〜0.10%の範囲である。
REM: 0.005-0.20%
REM refers to Sc, Y, and lanthanoid elements (elements up to atomic numbers 57 to 71 such as La, Ce, Pr, Nd, and Sm). REM improves the oxidation resistance by improving the adhesion of the Al 2 O 3 oxide film formed at high temperatures and reducing the formation rate. These effects can be obtained by adding 0.005% or more. On the other hand, if it exceeds 0.20%, it precipitates at the grain boundary of the slab and becomes the starting point of fracture. Therefore, the REM amount is in the range of 0.005 to 0.20%. Preferably it is 0.03 to 0.10% of range.
以上が本発明の高Al含有フェライト系ステンレス鋼板の基本化学成分であり、残部はＦｅおよび不可避的不純物からなる。更に、耐食性や高温強度向上の観点からMoおよびWのうち少なくとも一種を合計で0.10〜6.0%含有することができる。また、耐食性や耐酸化性向上の観点からCa:0.0005〜0.0200％、Mg:0.0002〜0.0200％のうち少なくとも1種を含有することができる。 The above are the basic chemical components of the high Al-containing ferritic stainless steel sheet of the present invention, and the balance consists of Fe and inevitable impurities. Furthermore, from the viewpoint of improving corrosion resistance and high temperature strength, at least one of Mo and W can be contained in a total amount of 0.10 to 6.0%. Further, from the viewpoint of improving corrosion resistance and oxidation resistance, at least one of Ca: 0.0005 to 0.0200% and Mg: 0.0002 to 0.0200% can be contained.
MoおよびWのうち少なくとも一種:合計で0.10〜6.0%
MoおよびWは鋼板の耐食性や高温強度を向上させる効果があるため、必要に応じて添加する。このような効果は、MoおよびWを合計で0.10%以上含有させることで得られる。一方、MoおよびWを合計で6.0%を超えて含有すると、スラブの靭性が著しく低下し、本発明の方法を用いても割れを防ぐことが困難となる。よって、含有する場合は、Mo量およびW量を合計で0.10〜6.0%の範囲とする。好ましくは2.5〜5.0%の範囲である。
At least one of Mo and W: 0.10-6.0% in total
Mo and W are added as necessary because they have the effect of improving the corrosion resistance and high temperature strength of the steel sheet. Such an effect is obtained by containing 0.10% or more of Mo and W in total. On the other hand, when Mo and W are contained in excess of 6.0% in total, the toughness of the slab is remarkably lowered, and it becomes difficult to prevent cracking even if the method of the present invention is used. Therefore, when it contains, let Mo amount and W amount be the range of 0.10 to 6.0% in total. Preferably it is 2.5 to 5.0% of range.
Ca:0.0005〜0.0200％、Mg:0.0002〜0.0200％
Ca、Mgは、鋼板の耐食性や耐酸化性を向上させる。これらの効果は、Caは0.0005％以上、Mgは0.0002％以上で得られる。しかし、これらの元素を各々0.0200％を超えて添加すると靭性の低下が起こる。よって、含有する場合は、Ca量は0.0005〜0.0200％、Mg量は0.0002〜0.0200％の範囲とする。好ましくは、それぞれ0.0010〜0.0050％の範囲である。
Ca: 0.0005-0.0200%, Mg: 0.0002-0.0200%
Ca and Mg improve the corrosion resistance and oxidation resistance of the steel sheet. These effects are obtained when Ca is 0.0005% or more and Mg is 0.0002% or more. However, when these elements are added in amounts exceeding 0.0200%, toughness is reduced. Therefore, when contained, the Ca content is in the range of 0.0005 to 0.0200%, and the Mg content is in the range of 0.0002 to 0.0200%. Preferably, it is 0.0010 to 0.0050% of range, respectively.
(2)ステンレス鋼板の表面状態
ステンレス鋼板の製造過程における歩留まり向上および製造効率向上のためには、熱間圧延または冷間圧延によって得られるステンレス鋼板の欠陥が少ないことが求められる。本発明の目的を達成するためには、鋼板圧延方向端部には、長さが20mm以上である端部割れが端部長さ1ｍ当たり1個以下である必要がある。端部割れの長さは次のよう定義する。鋼板表面と裏面で、それぞれ割れ起点（これは端部にある）と割れ先端を直線で結んでその距離を測る。割れが板厚方向に貫通していない等で鋼板の表面と裏面で長さが異なることがあるが、大きい値をその割れの長さとする。長さが20mm以上の端部割れは、熱間圧延後の工程でさらに大きな割れになったり、これが起点となって板が破断する場合がある。製造工程で板が破断すると歩留まりや製造効率が著しく低下する。さらには、製造ができなくなることもある。これを防ぐため、トリミングなどによってこの割れを除去するが、割れの部分だけを除去すると製造効率が大幅に低下し、全長にわたりトリミングを行うと歩留まり低下する。
(2) Surface condition of stainless steel plate In order to improve the yield and the production efficiency in the manufacturing process of the stainless steel plate, it is required that the stainless steel plate obtained by hot rolling or cold rolling has few defects. In order to achieve the object of the present invention, it is necessary that an end crack having a length of 20 mm or more is 1 or less per 1 m of the end length at the end in the steel sheet rolling direction. The length of the edge crack is defined as follows. On the front and back surfaces of the steel plate, measure the distance by connecting the crack starting point (which is at the end) and the crack tip with a straight line. Although the length may be different between the front surface and the back surface of the steel sheet because the crack does not penetrate in the thickness direction, a large value is defined as the length of the crack. An end crack having a length of 20 mm or more may become a larger crack in the process after hot rolling, or the plate may be broken starting from this. When the plate breaks during the manufacturing process, the yield and manufacturing efficiency are significantly reduced. Furthermore, it may become impossible to manufacture. In order to prevent this, the crack is removed by trimming or the like. However, if only the cracked portion is removed, the manufacturing efficiency is greatly reduced, and if the trimming is performed over the entire length, the yield is lowered.
また、鋼板表面は、圧延方向の長さが30mm以上かつ板厚深さ方向の長さが0.1mm以上の表面欠陥が5個/m2以下である必要がある。これを超える欠陥は、酸洗やグラインダー研磨など通常の工程では除去しきれず、最終製品に欠陥として残存しやすい。なお、長さ30ｍｍ以上に伸びた表面欠陥は、長さ30ｍｍ毎に１個と数えた。これらの欠陥を除去するためには、欠陥部分のみを重点的に削り取るか、鋼板を一部切断して欠陥を含む部分を板幅全長に渡って除去しなければならず、歩留まり低下や工程負荷の増大につながる。なお、表面欠陥とは割れ、ヘゲ、線ヘゲ等である。 Further, the steel sheet surface is required the length of the rolling direction is a length of 30mm or more and a thickness depth direction is more surface defects 0.1 mm 5 pieces / m 2 or less. Defects exceeding this cannot be removed by normal processes such as pickling and grinder polishing, and tend to remain as defects in the final product. In addition, the surface defect extended to 30 mm or more in length was counted as one for every 30 mm in length. In order to remove these defects, it is necessary to intensively scrape only the defective part, or to cut a part of the steel plate and remove the part including the defect over the entire length of the plate, resulting in a decrease in yield and process load. Leads to an increase in The surface defects are cracks, lashes, line lashes, and the like.
本発明の高Al含有フェライト系ステンレス冷延鋼板をさらに冷間圧延してステンレス箔とする場合、圧延回数や圧下率が大幅に増加するため、端部の割れや表面欠陥を起点とした破断や表面欠陥がより発生し易くなる。したがって、鋼板表面端部は圧延方向もしくは板幅方向に長さ10mm以上である端部割れが端部１ｍ当たり1個以下であり、鋼板表面には、圧延方向もしくは板幅方向の長さが10mm以上かつ板厚深さ方向の長さが0.05mm以上である表面欠陥が5個/m2以下であることが好ましい。このような高Al含有フェライト系ステンレス鋼板は、ステンレス箔として好適に用いることができる。 When the high Al content ferritic stainless steel cold rolled steel sheet of the present invention is further cold rolled into a stainless steel foil, the number of rolling and the rolling reduction are greatly increased. Surface defects are more likely to occur. Therefore, the edge of the steel plate has 10 or less edge cracks per 1 m of the end in the rolling direction or the plate width direction, and the length in the rolling direction or the plate width direction is 10 mm on the steel plate surface. The number of surface defects having a length in the thickness direction of 0.05 mm or more is preferably 5 / m 2 or less. Such a high Al content ferritic stainless steel sheet can be suitably used as a stainless steel foil.
(3)スラブ割れ防止方法
本発明では、鋼を、スラブもしくはインゴットに鋳造し、スラブに鋳造した場合は、スラブの表面温度が式（1）のT1℃もしくは式（２）のT2℃を下回る前に加熱炉に前記スラブを装入して加熱し、次いで熱間圧延する、インゴットに鋳造した場合は、インゴットの表面温度が式（1）のT1℃もしくは式（２）のT2℃を下回る前に加熱炉に前記インゴットを装入して加熱し、次いで分塊圧延する。
T1=4.5Cr％＋17Al％−50 式（1）
ただし、Cr％およびAl％は、それぞれCrあるいはAlの含有量(質量%)を表す。
T2=4.5Cr％＋17Al％＋6(Mo％＋W％)−50 式（2）
ただし、Cr％、Al％、Mo％およびW％は、それぞれCr、Al、Mo、Wの含有量(質量%)を表す。
このように、スラブもしくはインゴットの表面温度を制御してスラブもしくはインゴットを加熱炉に装入することでスラブ割れを抑制できる。以下、その抑制機構について説明する。
(3) Method for preventing slab cracking In the present invention, when steel is cast into a slab or ingot and cast into a slab, the surface temperature of the slab is T 1 ° C of formula (1) or T 2 ° C of formula (2). When the slab is placed in a heating furnace and heated and then hot-rolled before the temperature falls below, the surface temperature of the ingot is T 1 ° C of formula (1) or T of formula (2). Before the temperature falls below 2 ° C., the ingot is charged into the heating furnace and heated, and then subjected to split rolling.
T 1 = 4.5Cr% + 17Al% -50 Formula (1)
However, Cr% and Al% represent Cr or Al content (mass%), respectively.
T 2 = 4.5Cr% + 17Al% + 6 (Mo% + W%) − 50 Formula (2)
However, Cr%, Al%, Mo%, and W% represent the contents (mass%) of Cr, Al, Mo, and W, respectively.
Thus, slab cracking can be suppressed by controlling the surface temperature of the slab or ingot and charging the slab or ingot into the heating furnace. Hereinafter, the suppression mechanism will be described.
冷却可能限界温度
スラブを熱延加熱炉に装入する際の表面温度と冷延鋼板の表面形状との相関性を、実施例の項目にて後述する方法で調査した。その結果、表面形状に優れた高Al含有フェライト系ステンレス鋼板を得るために、スラブの表面温度が下回ってはならない温度、つまりスラブの冷却可能限界温度が存在することが明らかとなった。さらに、冷却可能限界温度と鋼成分との関係を調査した結果、以下の関係が成り立つことを見出した。
MoおよびWを含有しない場合、T1=4.5Cr％＋17Al％−50
MoあるいはWを含有する場合、T2=4.5Cr％＋17Al％＋6(Mo％＋W％)−50
ただし、T1あるいはT2は冷却可能限界温度（℃）、各元素記号はその成分元素の含有量(質量%)を表す。
The correlation between the surface temperature when charging the coolable limit temperature slab into the hot-rolling heating furnace and the surface shape of the cold-rolled steel sheet was investigated by the method described later in the item of Examples. As a result, in order to obtain a high Al-containing ferritic stainless steel sheet having an excellent surface shape, it has been clarified that there is a temperature at which the surface temperature of the slab must not fall, that is, a slab cooling limit temperature. Furthermore, as a result of investigating the relationship between the coolable limit temperature and the steel component, it was found that the following relationship holds.
When not containing Mo and W, T 1 = 4.5Cr% + 17Al% -50
When containing Mo or W, T 2 = 4.5Cr% + 17Al% + 6 (Mo% + W%)-50
However, T 1 or T 2 represents the cooling limit temperature (° C.), and each element symbol represents the content (mass%) of the component element.
スラブの表面温度がT1℃もしくはT2℃を下回ると、スラブ内部に割れが発生しやすくなり、割れが発生したスラブを熱間圧延さらには冷間圧延することで、熱延鋼板や冷延鋼板に欠陥が発生する。本式で示される温度を下回る前に熱延加熱炉に装入して再加熱することで、スラブに発生する割れを防止することができ、このスラブを圧延することで表面欠陥の少ない表面性状に優れた鋼板を得ることが可能となる。なお、上記はスラブから冷延鋼板を製造する場合であるが、インゴットから冷延鋼板を製造する場合も、スラブもしくはインゴットから熱延鋼板を製造する場合も同様の効果が得られることを確認した。 If the surface temperature of the slab falls below T 1 ° C or T 2 ° C, cracks are likely to occur inside the slab, and hot-rolled steel sheets and cold-rolled steel sheets are produced by hot-rolling and cold-rolling the cracked slab. Defects are generated in the steel sheet. It is possible to prevent cracks that occur in the slab by charging it in a hot rolling furnace before it falls below the temperature indicated by this formula, and it is possible to prevent cracks that occur in the slab. It is possible to obtain a steel plate excellent in the quality. In addition, although the above is a case where a cold-rolled steel sheet is manufactured from a slab, it has been confirmed that the same effect can be obtained when a cold-rolled steel sheet is manufactured from an ingot or when a hot-rolled steel sheet is manufactured from a slab or an ingot. .
スラブ冷却速度
前述の方法で求めた冷却可能限界温度T1℃あるいはT2℃を下回る前に加熱炉に装入して熱間圧延を実施することで、スラブ割れを防止し表面形状に優れた熱延鋼板を得ることができるが、より表面性状に優れた熱延鋼板を得るためには、鋳造後の冷却中に発生する熱応力を緩和することが好ましい。このためには加熱炉装入前のスラブあるいはインゴットに対して、500℃〜T0℃（500＞T0）の温度域を平均冷却速度：50℃/h以下で冷却することが好ましい。なお、T0℃は、加熱炉装入前のスラブ表面あるいはインゴット表面の最低温度である。平均冷却速度が50℃/hを超えた場合、内部に過大な熱応力が生じで微細な割れが発生し、熱延鋼板の表面欠陥が増加する場合がある。なお、500℃を超えた温度では組織に十分な延性が存在し、熱応力が発生しても破断に至る懸念はない。従って、より表面性状に優れた熱延鋼板を得るためには、500℃〜T0℃の間の平均冷却速度を50℃/h以下とすることが好ましい。さらなる熱応力の緩和が必要な場合は、500℃〜T0℃の間の平均冷却速度を30℃/h以下とすることがより好ましい。
Slab cooling rate The slab cracking was prevented and the surface shape was excellent by inserting into the heating furnace and carrying out hot rolling before the coolable limit temperature T 1 ℃ or T 2 ℃ obtained by the above method. Although a hot-rolled steel sheet can be obtained, in order to obtain a hot-rolled steel sheet with more excellent surface properties, it is preferable to relax the thermal stress generated during cooling after casting. For this purpose, it is preferable to cool the slab or ingot before charging the furnace at a temperature range of 500 ° C. to T 0 ° C. (500> T 0 ) at an average cooling rate of 50 ° C./h or less. T 0 ° C is the minimum temperature of the slab surface or ingot surface before charging the heating furnace. When the average cooling rate exceeds 50 ° C./h, excessive thermal stress is generated inside and fine cracks are generated, which may increase the surface defects of the hot-rolled steel sheet. It should be noted that when the temperature exceeds 500 ° C., the structure has sufficient ductility, and there is no concern that it will break even if thermal stress occurs. Therefore, in order to obtain a hot-rolled steel sheet having more excellent surface properties, the average cooling rate between 500 ° C. and T 0 ° C. is preferably 50 ° C./h or less. When further relaxation of thermal stress is necessary, it is more preferable that the average cooling rate between 500 ° C. and T 0 ° C. is 30 ° C./h or less.
製造方法
本発明の高Al含有フェライト系ステンレス鋼板は、通常のステンレス鋼板製造設備を用いて製造することができる。連続鋳造によって製造された鋼スラブ（インゴット）を大気中で放冷し、T1℃あるいはT2℃を下回る前に加熱炉に装入して熱間圧延（分塊圧延）して鋼板とする。より表面形状に優れた鋼板とするためには、表面温度が500℃〜T0℃の温度域を平均冷却速度50℃/h以下で冷却する。この場合、加熱炉や保温炉を用いて制御することができる。また、保温カバー等を被せてもよい。このように、スラブ（インゴット）をT1℃あるいはT2℃を下回る前に加熱炉に装入し、一般的な熱間圧延工程に供して熱延コイルとする。
Production Method The high Al-containing ferritic stainless steel sheet of the present invention can be produced using ordinary stainless steel sheet production equipment. Steel slabs (ingots) produced by continuous casting are allowed to cool in the atmosphere, and are inserted into a heating furnace before being below T 1 ℃ or T 2 ℃ and hot rolled (bundled rolling) to obtain steel plates. . In order to obtain a steel sheet having a more excellent surface shape, the temperature range of 500 ° C. to T 0 ° C. is cooled at an average cooling rate of 50 ° C./h or less. In this case, it can be controlled using a heating furnace or a heat-retaining furnace. Moreover, you may put a heat insulation cover etc. As described above, the slab (ingot) is charged into a heating furnace before the temperature falls below T 1 ° C or T 2 ° C, and is subjected to a general hot rolling process to form a hot rolled coil.
熱延コイルはそのまま製品として用いても良いし、その後冷間圧延によって冷延鋼板や箔などに加工して用いても良い。さらには、パイプ形状に加工されてもよいし、プレス加工などによって成型品として用いてもよい。本発明の鋼板は、高いAlを含有していることから、メタルハニカムの他、高温での耐酸化性が求められる部材に好適である。たとえば、自動車などの車両の排気系部材（エキゾーストマニホールド、コンバーターケース、マフラー、熱交換器、フレキシブルチューブなど）、暖房器具や燃焼器具の排気用部材などが挙げられるが、特にこれらの用途に限定されるものではない。 The hot rolled coil may be used as a product as it is, or may be used after being processed into a cold rolled steel sheet or foil by cold rolling. Furthermore, it may be processed into a pipe shape, or may be used as a molded product by pressing or the like. Since the steel sheet of the present invention contains high Al, it is suitable for a member that requires oxidation resistance at high temperature in addition to a metal honeycomb. For example, exhaust system members of vehicles such as automobiles (exhaust manifolds, converter cases, mufflers, heat exchangers, flexible tubes, etc.), exhaust members of heating appliances and combustion appliances, and the like are particularly limited. It is not something.
実施例に基づいて本発明を具体的に説明する。
表１の鋼記号A〜Pに示す化学組成の鋼を高周波真空炉で溶製し、約100mm×約100mm×約140mm高さの鋳片に鋳込んだ。凝固が完了したら鋳型から取り外し、直ちに1000℃に加熱した電気炉に装入した。鋳型から取り外した鋳片の表面温度はおよそ1000℃であった。鋼塊が電気炉に装入された後、電気炉を制御して500℃〜T℃までの冷却速度を25℃/h、45℃/h、 75℃/hの3種類で徐冷を行い、表2、3に記載した表面温度に達した時点で電気炉から取り出し、直ちに加熱炉に装入して再加熱を行った。1200℃で30分間均熱処理を行った後、熱間圧延して厚さ4mm幅140mm長さ約1800mmの熱延鋼板とした。なお、熱間圧延中に鋳片の底部と頭部は切り捨てた。
The present invention will be specifically described based on examples.
Steels having chemical compositions indicated by steel symbols A to P in Table 1 were melted in a high frequency vacuum furnace and cast into a slab having a height of about 100 mm × about 100 mm × about 140 mm. When solidification was completed, it was removed from the mold and immediately charged in an electric furnace heated to 1000 ° C. The surface temperature of the slab removed from the mold was about 1000 ° C. After the steel ingot is charged into the electric furnace, the electric furnace is controlled and the cooling rate from 500 ° C to T ° C is gradually cooled at three types of 25 ° C / h, 45 ° C / h and 75 ° C / h. When the surface temperatures listed in Tables 2 and 3 were reached, they were taken out of the electric furnace, immediately charged into the heating furnace, and reheated. After soaking at 1200 ° C. for 30 minutes, hot rolling was performed to obtain a hot rolled steel sheet having a thickness of 4 mm, a width of 140 mm, and a length of about 1800 mm. In addition, the bottom part and head part of the slab were discarded during hot rolling.
熱間圧延の途中に激しい割れが生じたものは、熱間圧延を中止してその後の評価は実施しなかった。 In the case where severe cracks occurred during the hot rolling, the hot rolling was stopped and the subsequent evaluation was not performed.
このようにして作製した熱延鋼板を長さ400mmに切断した。それぞれ1枚はそのままで、1枚は両端をトリミングして幅100mmとした後、1000℃で1分間保持する熱処理を行った。さらに、ショットブラストおよびフッ酸と硝酸の混合酸を用いた酸洗によって表面スケールを除去した後、冷間圧延を行って、板厚1mm幅140mm長さ約1600mmの冷延鋼板を得た。 The hot-rolled steel sheet thus produced was cut to a length of 400 mm. One piece was left as it was, and one piece was trimmed at both ends to a width of 100 mm, and then heat treatment was performed at 1000 ° C. for 1 minute. Further, after removing the surface scale by shot blasting and pickling using a mixed acid of hydrofluoric acid and nitric acid, cold rolling was performed to obtain a cold rolled steel sheet having a thickness of 1 mm, a width of 140 mm, and a length of about 1600 mm.
以上の方法で得られた熱延鋼板および冷延鋼板について、下記に示す方法で表面形状の評価を実施した。 About the hot-rolled steel plate and cold-rolled steel plate obtained by the above method, the surface shape was evaluated by the method shown below.
鋼板表面の割れや疵の有無を目視で調査し、鋼板端部の割れ(耳割れ)やそれ以外の表面欠陥が発見された場合、割れの長さおよび個数を測定した。熱延鋼板および冷延鋼板それぞれについて実施し、以下のように評価した。
◎（優れる）：長さ20mm以上の端部の割れ（耳割れ）が端部1ｍあたり１個以下、かつ、深さ0.1mm以上かつ圧延方向の長さ30mm以上の表面欠陥が1個/m2以下の場合
○（良好）：長さ20mm以上の端部の割れ（耳割れ）が端部1ｍあたり１個以下、かつ、深さ0.1mm以上かつ圧延方向の長さ30mm以上の表面欠陥が5個/m2以下の場合
△（不良）：長さ20mm以上の端部の割れ（耳割れ）が端部1ｍあたり１個超え、または、深さ0.1mm以上かつ圧延方向の長さ30mm以上の表面欠陥が5個/m2超えの場合
×（圧延中止）熱間圧延中もしくは冷間圧延中に激しい割れが生じ、圧延作業を中止したもの
なお、長さ30ｍｍ以上に伸びた表面欠陥は、長さ30ｍｍ毎に１個と数えた。
評価が、◎もしくは○であれば本発明の目的を達成し、良好な鋼板が得られるものと判断し合格とした。
以上の結果を表2、3に示す。
The presence or absence of cracks or flaws on the surface of the steel sheet was visually inspected, and when cracks at the edge of the steel sheet (ear cracks) or other surface defects were found, the length and number of cracks were measured. It implemented about each of a hot-rolled steel plate and a cold-rolled steel plate, and evaluated as follows.
◎ (Excellent): 1 or less surface defects with an edge crack (ear crack) of 20 mm or more in length per edge of 1 mm or less, a depth of 0.1 mm or more and a length of 30 mm or more in the rolling direction When 2 or less ○ (Good): Surface defects with a length of 20 mm or more at the end (ear cracks) of 1 or less per 1 m of edge, a depth of 0.1 mm or more and a length of 30 mm or more in the rolling direction When 5 pieces / m 2 or less △ (defect): The number of cracks (ear cracks) at the end of 20 mm or more exceeds 1 per 1 m of end, or the depth is 0.1 mm or more and the length in the rolling direction is 30 mm or more. If the surface defects of the steel exceeds 5 pieces / m 2 × (rolling discontinuation) During the hot rolling or cold rolling, severe cracks occurred and the rolling operation was discontinued. , One for every 30 mm in length.
If the evaluation was ◎ or ○, the object of the present invention was achieved, and it was judged that a good steel sheet was obtained, and it was determined as acceptable.
The results are shown in Tables 2 and 3.
表2、3より、スラブ表面温度がMoおよびWを含有しない場合、T1=4.5Cr％＋17Al％−50、MoあるいはWを含有する場合、T2=4.5Cr％＋17Al％＋6(Mo％＋W％)−50で計算される温度を下回る前に再加熱して製造した試験片は、熱延鋼板が◎もしくは○の評価で、良好な鋼板を得ることができた。特に、スラブ冷却速度を45℃/hとした場合は、75℃/hとした場合に比べて、より多くの試験片（鋼板）において◎の評価が得られた。鋼記号E、K、L、MのようなT1もしくはT2計算値が150℃を超えるような鋼板においては、さらに冷却速度を低下させて25℃/hとすることで、◎（優れる）の評価が得られた。 From Tables 2 and 3, when the slab surface temperature does not contain Mo and W, T 1 = 4.5Cr% + 17Al% −50, and when Mo or W is contained, T 2 = 4.5Cr% + 17Al% + 6 (Mo% + W %) The test piece manufactured by reheating before falling below the temperature calculated by −50 was able to obtain a good steel plate with a hot-rolled steel plate evaluated as “◎” or “○”. In particular, when the slab cooling rate was 45 ° C./h, more evaluations of “◎” were obtained for more test pieces (steel plates) than when the slab cooling rate was 75 ° C./h. For steel plates such as steel symbols E, K, L, and M where the calculated value of T 1 or T 2 exceeds 150 ° C, the cooling rate can be further reduced to 25 ° C / h, resulting in ◎ (excellent) Was obtained.
一方、成分が本発明範囲外の鋼記号N、O、Pでは、熱間圧延中に激しい割れが生じたため作業を中止し×（不良）評価とした。 On the other hand, in steel symbols N, O, and P whose components are out of the scope of the present invention, since severe cracks occurred during hot rolling, the operation was stopped and evaluated as x (defective).
成分は本発明範囲内であるが加熱炉で再加熱した際のスラブ表面温度がT1もしくはT2計算値を下回る試験片No.49〜64の鋼板では、No.59〜64の鋼板が熱間圧延中に激しい割れが生じたため作業を中止し×（不良）評価とした。また、Ｎｏ．50、54、55および58の鋼板では、トリミングをしていない板が冷間圧延中に激しい割れが生じたため作業を中止し×（不良）評価とした。Ｎｏ．49、52、56および57の鋼板は、冷間圧延材の評価が△（不良）の評価であった。 The steel specimens No.49~64 component slab surface temperature when it is within the present invention ranges reheated in a heating furnace is lower than the T 1 or T 2 calculated values, the steel sheet of No.59~64 heat Since severe cracks occurred during hot rolling, the operation was stopped and evaluated as x (defect). No. In the steel sheets of 50, 54, 55 and 58, the untrimmed plate was severely cracked during cold rolling, so the operation was stopped and evaluated as x (defect). No. Regarding the steel sheets of 49, 52, 56 and 57, the evaluation of the cold rolled material was an evaluation of Δ (defect).
以上の結果より、本発明では、鋳片割れを防止し表面性状に優れた高Ａｌ含有フェライト系ステンレス鋼板を得ることが可能となった。 From the above results, according to the present invention, it is possible to obtain a high Al-containing ferritic stainless steel sheet having excellent surface properties by preventing slab cracking.
Claims (9)
鋼板圧延方向端部には、長さが20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下である
ことを特徴とする高Al含有フェライト系ステンレス鋼板。 As component composition, in mass%, C: 0.001 to 0.050%, Si: 0.01 to 2.0%, Mn: 0.01 to 1.0%, S: 0.01% or less, P: 0.05% or less, Cr: 15.0 to 30.0%, Ni: Contains 0.01 to 0.60%, Al: 2.5 to 6.5%, N: 0.001 to 0.050%, Ti: 0.01 to 0.30%, Nb: 0.01 to 0.30%, Zr: 0.005 to 0.20%, Hf: 0.005 to 0.20 %, REM: contain 0.005 to 0.20% or more, the balance consists of Fe and inevitable impurities,
At the end in the rolling direction of the steel sheet, the number of end cracks having a length of 20 mm or more is 1 or less per 1 m of end length, and the length in the rolling direction is 30 mm or more in the thickness direction of the steel sheet. A high Al-containing ferritic stainless steel sheet characterized in that the number of surface defects having a length of 0.1 mm or more is 5 / m 2 or less.
スラブに鋳造した場合は、スラブの表面温度が式（1）のT1℃を下回る前に加熱炉に前記スラブを装入して加熱し、次いで熱間圧延する、
インゴットに鋳造した場合は、インゴットの表面温度が式（1）のT1℃を下回る前に加熱炉に前記インゴットを装入して加熱し、次いで分塊圧延し熱間圧延する
ことを特徴とする、
鋼板圧延方向端部には、20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下である高Al含有フェライト系ステンレス鋼板の製造方法。
T1=4.5Cr％＋17Al％−50 式（1）
ただし、Cr％およびAl％は、それぞれCrあるいはAlの含有量(質量%)を表す。 Casting steel comprising the component composition of claim 1 into a slab or ingot,
When cast into a slab, the slab is charged and heated in a heating furnace before the surface temperature of the slab falls below T 1 ° C of formula (1), and then hot-rolled.
When cast into an ingot, the ingot is charged in a heating furnace and heated before the surface temperature of the ingot falls below T 1 ° C. of the formula (1), and then it is split-rolled and hot-rolled. To
At the end in the rolling direction of the steel plate, there are no more than 1 crack per 1 m of the end length per 1 m of the end length, and the length in the rolling direction is 30 mm or more and the length in the thickness direction of the steel plate. high Al content production method of ferritic stainless steel sheet surface defects is 0.1mm or more is 5 / m 2 or less.
T 1 = 4.5Cr% + 17Al% -50 Formula (1)
However, Cr% and Al% represent Cr or Al content (mass%), respectively.
スラブに鋳造した場合は、スラブの表面温度が式（２）のT2℃を下回る前に加熱炉に前記スラブを装入して加熱し、次いで熱間圧延する
インゴットに鋳造した場合は、インゴットの表面温度が式（２）のT2℃を下回る前に加熱炉に前記インゴットを装入して加熱し、次いで分塊圧延し熱間圧延する
ことを特徴とする、
鋼板圧延方向端部には、長さが20ｍｍ以上である端部割れが端部長さ１ｍ当たり1個以下であり、鋼板表面には、圧延方向の長さが30ｍｍ以上かつ板厚深さ方向に長さが0.1ｍｍ以上である表面欠陥が5個/ｍ2以下である高Al含有フェライト系ステンレス鋼板の製造方法。
T2=4.5Cr％＋17Al％＋6(Mo％＋W％)−50 式（2）
ただし、Cr％、Al％、Mo％およびW％は、それぞれCr、Al、Mo、Wの含有量(質量%)を表す。 Casting the steel comprising the composition of claim 2 into a slab or ingot,
When cast into a slab, when the slab is cast into an ingot that is heated and then hot-rolled before the surface temperature of the slab falls below T 2 ° C in formula (2), then ingot Before the surface temperature of T2 of formula (2) falls below T 2 ° C., the ingot is charged into the heating furnace and heated, and then it is split-rolled and hot-rolled.
At the end in the rolling direction of the steel sheet, the number of end cracks having a length of 20 mm or more is 1 or less per 1 m of end length, and the length in the rolling direction is 30 mm or more in the thickness direction of the steel sheet. A method for producing a high Al-containing ferritic stainless steel sheet having a length of 0.1 mm or more and surface defects of 5 pieces / m 2 or less.
T 2 = 4.5Cr% + 17Al% + 6 (Mo% + W%) − 50 Formula (2)
However, Cr%, Al%, Mo%, and W% represent the contents (mass%) of Cr, Al, Mo, and W, respectively.
ただし、前記T0℃は、加熱炉挿入前のスラブ表面あるいはインゴット表面の最低温度である。 The temperature range of 500 ° C. to T 0 ° C. is cooled at an average cooling rate of 50 ° C./h or less with respect to the slab or the ingot before the heating furnace is inserted. The manufacturing method of the high Al content ferritic stainless steel sheet as described in a term.
However, T 0 ° C. is the minimum temperature of the slab surface or ingot surface before inserting the heating furnace.
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| WO2020170628A1 (en) * | 2019-02-19 | 2020-08-27 | Ｊｆｅスチール株式会社 | FERRITE STAINLESS STEEL SHEET, PRODUCTION METHOD FOR SAME, AND STAINLESS STEEL SHEET HAVING Al VAPOR-DEPOSITED LAYER |
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| JPH04362127A (en) * | 1991-06-10 | 1992-12-15 | Nisshin Steel Co Ltd | Production of ferritic stainless steel strip having high al content |
| JPH0820847A (en) * | 1994-07-06 | 1996-01-23 | Nisshin Steel Co Ltd | Production of high aluminum-containing ferritic stainless steel |
| JP2005089850A (en) * | 2003-09-19 | 2005-04-07 | Nisshin Steel Co Ltd | High strength ferritic stainless steel |
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| WO2020170628A1 (en) * | 2019-02-19 | 2020-08-27 | Ｊｆｅスチール株式会社 | FERRITE STAINLESS STEEL SHEET, PRODUCTION METHOD FOR SAME, AND STAINLESS STEEL SHEET HAVING Al VAPOR-DEPOSITED LAYER |
| CN113383103A (en) * | 2019-02-19 | 2021-09-10 | 杰富意钢铁株式会社 | Ferritic stainless steel sheet, method for producing same, and stainless steel sheet with Al deposited layer |
| EP3929322A4 (en) * | 2019-02-19 | 2022-12-07 | JFE Steel Corporation | Ferrite stainless steel sheet, production method for same, and stainless steel sheet having al vapor-deposited layer |
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