JP2002097552A - Hot-dip plated ferritic stainless-steel sheet for fuel tank and manufacturing method therefor - Google Patents
Hot-dip plated ferritic stainless-steel sheet for fuel tank and manufacturing method thereforInfo
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- JP2002097552A JP2002097552A JP2000282978A JP2000282978A JP2002097552A JP 2002097552 A JP2002097552 A JP 2002097552A JP 2000282978 A JP2000282978 A JP 2000282978A JP 2000282978 A JP2000282978 A JP 2000282978A JP 2002097552 A JP2002097552 A JP 2002097552A
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- steel sheet
- hot
- ferritic stainless
- stainless steel
- fuel tank
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、自動車用をはじめ
とする燃料タンク用素材として使用可能な溶融めっきフ
ェライト系ステンレス鋼板およびその製造方法に関する
ものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a hot-dip ferritic stainless steel sheet which can be used as a material for fuel tanks such as automobiles and a method for producing the same.
【０００２】[0002]
【従来の技術】自動車の燃料タンクは形状が複雑である
ため、素材には優れたプレス成形性が要求される。また
海岸近くの走行や融雪剤を散布された道路の走行が想定
されるため、燃料タンク用素材には塩害環境での優れた
耐食性が要求される。さらにガソリン等の燃料による腐
食も懸念されることから、素材は燃料による耐食性も優
れる必要がある。このような要求を満足する素材とし
て、従来は低炭素鋼の深絞り鋼板あるいは超深絞り鋼板
にアルミニウム系あるいは鉛系などのめっきを施した表
面処理鋼板が使用されてきた。2. Description of the Related Art Since fuel tanks of automobiles are complicated in shape, raw materials are required to have excellent press formability. Further, since it is assumed that the vehicle runs near the coast or on a road on which a snow melting agent has been sprayed, the material for the fuel tank is required to have excellent corrosion resistance in a salt damage environment. Further, since there is a concern about corrosion due to fuel such as gasoline, the material needs to have excellent corrosion resistance due to fuel. As a material that satisfies such requirements, conventionally, a surface-treated steel sheet obtained by plating a deep-drawn steel sheet of ultra-low carbon steel or an ultra-deep-drawn steel sheet with an aluminum-based or lead-based steel has been used.
【０００３】近年、環境保持の観点から自動車には従来
よりも長寿命が求められている。その結果、自動車の構
成部品の一つである燃料タンクに対してもより長寿命が
要求されており、従来の表面処理鋼板では耐食性が不十
分になってきている。そこで耐食性を高めるために、め
っき原板として従来の低炭素鋼の代わりにフェライト系
ステンレス鋼板を適用することが望まれている。しかし
ながら、主に建材用途に使用されている従来の溶融めっ
きフェライト系ステンレス鋼板は伸びが小さいため、プ
レス成形性がやや劣るという問題点がある。In recent years, from the viewpoint of environmental preservation, automobiles are required to have a longer life than before. As a result, a longer life is required for a fuel tank, which is one of the components of an automobile, and the conventional surface-treated steel sheet has become insufficient in corrosion resistance. Therefore, in order to enhance the corrosion resistance, it is desired to use a ferritic stainless steel sheet instead of a conventional low carbon steel sheet as a plating base sheet. However, the conventional hot-dip-coated ferritic stainless steel sheet mainly used for building materials has a small elongation, and thus has a problem that press formability is slightly inferior.
【０００４】[0004]
【発明が解決しようとする課題】本発明の課題は、自動
車用のような複雑形状の燃料タンクにプレス成形可能で
あり、さらに塩害環境での耐食性や燃料による耐食性が
長期間にわたり優れる燃料タンク用溶融めっきフェライ
ト系ステンレス鋼板およびその製造方法を提供すること
にある。SUMMARY OF THE INVENTION An object of the present invention is to provide a fuel tank which can be press-molded into a fuel tank having a complicated shape such as an automobile, and which has excellent corrosion resistance in a salt damage environment and corrosion resistance due to fuel for a long period of time. An object of the present invention is to provide a hot-dip ferritic stainless steel sheet and a method for producing the same.
【０００５】[0005]
【課題を解決するための手段】本発明者らは、溶融めっ
きフェライト系ステンレス鋼板のプレス成形性および塩
害環境での耐食性や燃料による耐食性に及ぼす合金元
素、製造方法の影響などを詳細に検討した。その結果、
めっき原板となるフェライト系ステンレス鋼のＣｒ量、
Ｃ量、Ｎ量およびＴｉ、Ｎｂ量を限定し、さらに冷間圧
延後の焼鈍温度もしくは冷間圧延の累積圧下率を限定す
ることが有効であることを見出し、本発明を完成した。
すなわち本発明の要旨は次の通りである。（１）質量％
で、 Ｃｒ：１０．５〜１２％、 Ｃ≦０．０１５％、 Ｎ≦
０．０１％、Ｔｉ，Ｎｂの１種もしくは２種を（Ｔｉ＋
Ｎｂ）／（Ｃ＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス鋼板をめっきの原板とし、
伸びが３２％以上、平均ｒ値が１．４以上であることを
特徴とする燃料タンク用溶融めっきフェライト系ステン
レス鋼板。（２）質量％で、 Ｃｒ：１０．５〜１２％、 Ｃ≦０．０１５％、 Ｎ≦
０．０１％、Ｔｉ，Ｎｂの１種もしくは２種を（Ｔｉ＋
Ｎｂ）／（Ｃ＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス冷延鋼板を、７５０℃以上
で仕上焼鈍した後に溶融めっきを施すことを特徴とする
燃料タンク用溶融めっきフェライト系ステンレス鋼板の
製造方法。（３）質量％で、 Ｃｒ：１０．５〜１２％、 Ｃ≦０．０１５％、 Ｎ≦
０．０１％、Ｔｉ，Ｎｂの１種もしくは２種を（Ｔｉ＋
Ｎｂ）／（Ｃ＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス熱延鋼板を、累積圧下率７
０％以上で冷間圧延し、さらに仕上焼鈍した後に溶融め
っきを施すことを特徴とする燃料タンク用溶融めっきフ
ェライト系ステンレス鋼板の製造方法。Means for Solving the Problems The present inventors have examined in detail the press formability of hot-dip-coated ferritic stainless steel sheets, the effects of alloying elements on corrosion resistance in a salt-damaged environment and corrosion resistance due to fuel, and the effects of manufacturing methods. . as a result,
Cr content of ferritic stainless steel as plating base sheet,
The inventors have found that it is effective to limit the amounts of C, N, Ti and Nb, and further limit the annealing temperature after cold rolling or the cumulative rolling reduction of cold rolling, and completed the present invention.
That is, the gist of the present invention is as follows. (1) mass%
Where: Cr: 10.5 to 12%, C ≦ 0.015%, N ≦
0.01%, one or two of Ti and Nb (Ti +
Nb) / (C + N) ≧ 8, with the balance being a ferrite stainless steel sheet composed of Fe and unavoidable impurities,
A hot-dip ferritic stainless steel sheet for a fuel tank, having an elongation of at least 32% and an average r value of at least 1.4. (2) In mass%, Cr: 10.5 to 12%, C ≦ 0.015%, N ≦
0.01%, one or two of Ti and Nb (Ti +
Nb) / (C + N) ≧ 8, a ferritic stainless steel cold-rolled steel sheet containing Fe and unavoidable impurities with the balance being finish-annealed at 750 ° C. or more and then subjected to hot-dip plating. For producing hot-dip ferritic stainless steel sheet. (3) In mass%, Cr: 10.5 to 12%, C ≦ 0.015%, N ≦
0.01%, one or two of Ti and Nb (Ti +
Nb) / (C + N) ≧ 8, the balance being Fe and stainless steel unavoidable impurities.
A method for producing a hot-dip ferritic stainless steel sheet for a fuel tank, wherein the hot-rolled ferritic stainless steel sheet for a fuel tank is cold-rolled at 0% or more, and then finish-annealed.
【０００６】[0006]
【発明の実施の形態】以下に本発明を詳細に説明する。
初めに本発明の成分限定範囲について述べる。成分含有
量は質量％である。 Ｃｒ：１０．５％以上で１２％以下とする必要がある。
塩害環境での耐食性や燃料による耐食性を保持するため
にはめっき原板の耐食性が要求され、そのためには１
０．５％以上の含有が必要である。しかしながら１２％
を超えて含有すると鋼板の伸び、ｒ値が低下し、プレス
成形性が劣化するため、上限を１２％以下とする必要が
ある。DESCRIPTION OF THE PREFERRED EMBODIMENTS The present invention will be described below in detail.
First, the component limitation range of the present invention will be described. The component content is% by mass. Cr: It is necessary to be not less than 10.5% and not more than 12%.
In order to maintain the corrosion resistance in a salt damage environment or the corrosion resistance due to fuel, the corrosion resistance of the plating base sheet is required.
A content of 0.5% or more is required. However, 12%
If the content exceeds 0.005%, the elongation and r-value of the steel sheet decrease, and the press formability deteriorates. Therefore, the upper limit needs to be 12% or less.
【０００７】Ｃ：０．０１５％以下とする必要がある。
優れたプレス成形性を得るためにはめっき原板の加工性
を高めることが必要である。めっき原板のＣが低いほど
伸び、ｒ値が向上する。燃料タンクへのプレス成形を可
能とするには、上限を０．０１５％以下としなければな
らない。C: It is necessary to be 0.015% or less.
In order to obtain excellent press formability, it is necessary to enhance the workability of the original plate. The lower the C of the original plating, the higher the elongation and the higher the r value. In order to enable press forming to a fuel tank, the upper limit must be 0.015% or less.
【０００８】Ｎ：０．０１％以下とする必要がある。優
れたプレス成形性を得るためにはめっき原板の加工性を
高めることが必要である。めっき原板のＮが低いほど伸
び、ｒ値が向上する。燃料タンクへのプレス成形を可能
とするには、上限を０．０１％以下としなければならな
い。N: It is necessary to be 0.01% or less. In order to obtain excellent press formability, it is necessary to enhance the workability of the original plate. The lower the N of the plating base sheet, the longer the elongation and the higher the r value. In order to enable press molding into a fuel tank, the upper limit must be 0.01% or less.
【０００９】Ｔｉ，Ｎｂ：１種もしくは２種をＴｉ＋Ｎ
ｂとして、Ｃ＋Ｎの８倍以上とする必要がある。優れた
プレス成形性を得るためにはめっき原板の加工性を高め
ることが必要である。めっき原板中のＴｉやＮｂはＣ，
Ｎと容易に結合し、鋼中に固溶するＣ，Ｎ量を実質的に
低減する作用があり、その結果、プレス成形性を高める
ことができる。この効果はＴｉ＋Ｎｂとして８×（Ｃ＋
Ｎ）未満の含有量では不十分である。Ti, Nb: One or two of Ti + N
b needs to be at least 8 times C + N. In order to obtain excellent press formability, it is necessary to enhance the workability of the original plate. Ti and Nb in the original plate are C,
It easily bonds with N and has the effect of substantially reducing the amounts of C and N dissolved in steel as a solid solution. As a result, press formability can be improved. This effect is 8 × (C +
Content below N) is not sufficient.
【００１０】Ｓｉについては特に成分範囲を限定しない
が、低減すれば伸び、ｒ値が向上し、プレス成形性をさ
らに高めることができる。不可避的に混入するが、０．
６％以下の添加は許容できる。さらに０．２％以下とす
ることで溶融めっき性が向上する。Regarding Si, the component range is not particularly limited. However, when Si is reduced, elongation and r value are improved, and press formability can be further enhanced. Although inevitably mixed, 0.
Additions of 6% or less are acceptable. Further, when the content is 0.2% or less, the hot-dip plating property is improved.
【００１１】Ｍｎについては特に成分範囲を限定しない
が、低減すれば伸び、ｒ値が向上し、プレス成形性をさ
らに高めることができる。不可避的に混入するが、０．
５％以下の添加は許容できる。Although there is no particular limitation on the component range of Mn, if it is reduced, elongation and r value are improved, and press formability can be further enhanced. Although inevitably mixed, 0.
Additions of 5% or less are acceptable.
【００１２】Ｐについては特に成分範囲を限定しない
が、低減すれば伸び、ｒ値が向上し、プレス成形性をさ
らに高めることができる。不可避的に混入するが、０．
０４％以下の添加は許容できる。[0012] The component range of P is not particularly limited. However, when P is reduced, elongation and r value are improved, and press formability can be further enhanced. Although inevitably mixed, 0.
Additions of up to 04% are acceptable.
【００１３】Ｓについては特に成分範囲を限定しない
が、低減すれば伸び、ｒ値が向上し、プレス成形性をさ
らに高めることができる。不可避的に混入するが、０．
０１％以下の添加は許容できる。Although there is no particular limitation on the component range of S, if it is reduced, elongation and r-value are improved, and press formability can be further improved. Although inevitably mixed, 0.
Addition of up to 01% is acceptable.
【００１４】またＡｌは、製鋼において脱酸剤として使
用するため、不可避的に０．０４〜０．１０％程度含ま
れるが、このような範囲では成形性、耐食性に及ぼす影
響が小さいため、本発明では特に限定しない。Al is inevitably contained in an amount of about 0.04 to 0.10% because it is used as a deoxidizing agent in steelmaking. However, in such a range, Al has little effect on formability and corrosion resistance. The invention is not particularly limited.
【００１５】次に、プレス成形性指標に関する限定範囲
について述べる。溶融めっきフェライト系ステンレス鋼
板の伸びは３２％以上、平均ｒ値は１．４以上必要であ
る。複雑形状でありさらに張出し成形、深絞り成形が混
在した燃料タンクへのプレス成形に際しては、張出し成
形性の指標である伸びが３２％以上、深絞り成形の指標
である平均ｒ値が１．４以上なければ割れが発生してし
まう。Next, the limited range relating to the press formability index will be described. The elongation of the hot-dip ferritic stainless steel sheet must be 32% or more, and the average r value must be 1.4 or more. In press forming to a fuel tank having a complex shape and also a mixture of stretch forming and deep drawing, elongation as an index of stretch forming property is 32% or more, and an average r value as an index of deep drawing is 1.4. Otherwise, cracks will occur.
【００１６】さらに、製造方法に関する限定範囲につい
て述べる。溶融めっきフェライト系ステンレス鋼板の伸
びを３２％以上とするためには、上記成分範囲のフェラ
イト系ステンレス鋼冷延鋼板を７５０℃以上で仕上焼鈍
した後に溶融めっきを施すことが有効である。図１に、
実験室で製作したＣｒ：１０．８％、Ｃ：０．００４
％、Ｎ：０．００６％、Ｔｉ：０．１５％を含有し、板
厚が０．８mmのフェライト系ステンレス冷延鋼板の仕上
焼鈍温度を変化させ、仕上焼鈍後にＡｌを主成分とする
溶融めっきを施した溶融めっき鋼板の全伸びを測定した
結果を示す。仕上焼鈍温度の上昇と共に溶融めっき鋼板
の伸びは向上し、仕上焼鈍温度が７５０℃以上の範囲で
３２％以上の全伸びが得られる。これは仕上焼鈍温度の
上昇により、めっき原板であるフェライト系ステンレス
鋼板の結晶粒径が大きくなるためと考えられる。Further, a limited range of the manufacturing method will be described. In order to increase the elongation of the hot-dip ferritic stainless steel sheet to 32% or more, it is effective to subject the ferritic stainless steel cold-rolled steel sheet having the above component range to finish annealing at 750 ° C. or more, and then to apply hot-dip plating. In FIG.
Cr produced in the laboratory: 10.8%, C: 0.004
%, N: 0.006%, Ti: 0.15%, the finish annealing temperature of a ferritic stainless steel cold-rolled steel sheet having a thickness of 0.8 mm is changed, and after the finish annealing, melting mainly containing Al is performed. The result of having measured the total elongation of the hot-dip coated steel sheet subjected to plating is shown. The elongation of the hot-dip coated steel sheet increases with an increase in the finish annealing temperature, and a total elongation of 32% or more is obtained when the finish annealing temperature is 750 ° C. or more. It is considered that this is because the crystal grain size of the ferritic stainless steel sheet, which is the original plate for plating, increases with an increase in the finish annealing temperature.
【００１７】溶融めっきフェライト系ステンレス鋼板の
平均ｒ値を１．４以上とするためには、上記成分範囲の
フェライト系ステンレス鋼熱延鋼板を累積圧下率７０％
以上で冷間圧延し、さらに仕上焼鈍した後に溶融めっき
を施すことが有効である。図２に、実験室で製作したＣ
ｒ：１０．８％、Ｃ：０．００４％、Ｎ：０．００６
％、Ｔｉ：０．１５％を含有するフェライト系ステンレ
ス熱延鋼板を、累積圧下率を変化させて冷延した後に仕
上焼鈍し、さらにＡｌを主成分とする溶融めっきを施し
た溶融めっき鋼板の平均ｒ値を測定した結果を示す。冷
間圧延の累積圧下率が上昇すると共に溶融めっき鋼板の
平均ｒ値は向上し、冷間圧延の累積圧下率が７０％以上
の範囲で１．４以上の平均ｒ値が得られる。これは冷間
圧延の累積圧下率の上昇により、めっき原板であるフェ
ライト系ステンレス鋼板の集合組織が発達するためと考
えられる。In order to set the average r value of the hot-dip coated ferritic stainless steel sheet to 1.4 or more, the hot-rolled ferritic stainless steel sheet having the above-mentioned component range must have a cumulative rolling reduction of 70%.
It is effective to apply hot-dip plating after cold rolling and finish annealing as described above. FIG. 2 shows the C produced in the laboratory.
r: 10.8%, C: 0.004%, N: 0.006
%, Hot-rolled ferritic stainless steel sheet containing 0.15% of Ti, cold-rolled by changing the cumulative rolling reduction, then finish annealing, and further hot-dip coated steel sheet mainly containing Al. The result of measuring the average r value is shown. As the cumulative rolling reduction of the cold rolling increases, the average r value of the hot-dip coated steel sheet improves, and an average r value of 1.4 or more is obtained when the cumulative rolling reduction of the cold rolling is 70% or more. It is considered that this is because the texture of the ferritic stainless steel sheet, which is the original plate for plating, develops due to the increase in the cumulative draft of the cold rolling.
【００１８】[0018]
【実施例】表１に示す化学成分を有する７種のフェライ
ト系ステンレス鋼Ａ〜Ｇを溶製し、連続鋳造により２５
０mm厚の鋳片とした。表１において、Ｎｂについての
「−」印は、積極的には添加していないことを示す。但
し、０．０１％程度は不可避的不純物として鋼中に混入
している。次に表２に示すように、これらの鋳片を熱延
厚を変化させて熱間圧延し熱延コイルとした。次に冷間
圧延では熱延厚に応じて累積圧下率を変化させ、全て
０．８mm厚の冷延コイルとした。そして温度を変化させ
て仕上焼鈍を施した。最後にＡｌを主成分とする溶融め
っきを施した。EXAMPLE Seven types of ferritic stainless steels A to G having the chemical components shown in Table 1 were melted and continuously cast to obtain 25%.
It was a slab having a thickness of 0 mm. In Table 1, the "-" mark for Nb indicates that it was not added positively. However, about 0.01% is mixed in steel as inevitable impurities. Next, as shown in Table 2, these cast pieces were hot-rolled by changing the hot-rolled thickness to obtain hot-rolled coils. Next, in the cold rolling, the cumulative rolling reduction was changed in accordance with the thickness of the hot rolled sheet, and all the cold rolled coils were 0.8 mm thick. And the finish annealing was given by changing the temperature. Finally, hot-dip plating containing Al as a main component was performed.
【００１９】得られた溶融めっきフェライト系ステンレ
ス鋼板からＪＩＳ１３Ｂ号引張試験片を切出し、伸びを
測定した。またＪＩＳ５号引張試験片を切出し、１５％
の歪を付与した後に平均ｒ値を測定した。なお、表２に
おいて平均ｒ値が「−」印となっているのは、伸びが小
さいため１５％歪を付与する前に試験片が破断してしま
った場合である。A JIS No. 13B tensile test piece was cut out from the obtained hot-dip ferritic stainless steel sheet, and the elongation was measured. In addition, cut out JIS No. 5 tensile test piece, 15%
The average r value was measured after applying a strain of. In Table 2, the average r-value is marked with a “-” mark when the test piece was broken before 15% strain was applied due to small elongation.
【００２０】また、得られた溶融めっきフェライト系ス
テンレス鋼板を用いて、自動車の燃料タンク用材への適
用性を評価するため、次の試験を実施した。プレス成形
性の評価として、実際の燃料タンク形状にプレス成形し
た。この際、タンク形状としてはプレス成形形態が異な
るタイプ１、２の２種を用いた。タイプ１は主に張出し
成形性が要求される形状、タイプ２は主に深絞り成形性
が要求される形状である。評価は、問題なく所定の形状
にプレスできた場合を○、割れなく所定の形状にプレス
できたものの一部にくびれが発生した場合を△、割れが
発生したものを×とした。The following test was conducted to evaluate the applicability of the obtained hot-dip ferritic stainless steel sheet to fuel tank materials for automobiles. As an evaluation of press formability, press forming was performed into an actual fuel tank shape. At this time, as the tank shape, two types, types 1 and 2 having different press molding forms were used. Type 1 is a shape that mainly requires stretch formability, and type 2 is a shape that mainly requires deep drawability. The evaluation was evaluated as ○ when the sample was pressed into a predetermined shape without any problem, Δ when the neck was partially formed in the sample that was pressed into the predetermined shape without crack, and × when the sample was cracked.
【００２１】塩害環境での耐食性評価として、５０℃の
５重量％ＮａＣｌ溶液を用い、スプレー噴霧→乾燥→浸
漬→乾燥のサイクルを１日間で行うサイクル腐食試験を
１００日間続けて実施した後、腐食による最大侵食深さ
を測定した。評価は、最大侵食深さが初期板厚の１／２
以下である場合を○、最大侵食深さが初期板厚の１／２
以上ではあるが板厚貫通に至っていない場合を△、侵食
が板厚を貫通した場合を×とした。As an evaluation of corrosion resistance in a salt damage environment, a cycle corrosion test in which a 5% by weight NaCl solution at 50 ° C. is performed in a spray spray → dry → dip → dry cycle in one day is continuously performed for 100 days. The maximum erosion depth due to was measured. The evaluation shows that the maximum erosion depth is の of the initial thickness.
場合 when less than or equal to, maximum erosion depth is の of initial plate thickness
As described above, the case where the sheet thickness did not penetrate was indicated by Δ, and the case where erosion penetrated the sheet thickness was indicated by ×.
【００２２】燃料による耐食性評価として、劣化ガソリ
ンに蒸留水を１０％含有させた液中に薄鋼板を２８日間
浸漬した後、薄鋼板の腐食状況を調査した。評価は外観
に大きな変化がない場合を○、外観に大きな変化がある
が錆が発生していない場合を△、錆が発生した場合を×
とした。以上に示したプレス成形性評価、耐食性評価結
果を併せて表２に示す。As an evaluation of corrosion resistance by fuel, a steel sheet was immersed in a liquid containing 10% distilled water in deteriorated gasoline for 28 days, and then the corrosion state of the steel sheet was examined. The evaluation was を when there was no significant change in appearance, △ when there was a large change in appearance but no rust occurred, and × when rust occurred.
And Table 2 also shows the results of the press formability evaluation and the corrosion resistance evaluation described above.
【００２３】[0023]
【表１】 [Table 1]
【００２４】[0024]
【表２】 [Table 2]
【００２５】表２から、本発明例であるＮｏ．１，３，
５，６はプレス成形性、耐食性ともに優れ、自動車の燃
料タンク用材として適用可能なことが分かる。同じ鋼Ａ
を用いたＮｏ．１とＮｏ．２とを比較すると、７５０℃
以上で仕上焼鈍したＮｏ．１が３６％の全伸びとなり、
プレス成形性が優れているのに対し、７５０℃未満で仕
上焼鈍したＮｏ．２は全伸びが１３％しかなく、燃料タ
ンクへのプレス成形時に割れが発生した。また同様にＮ
ｏ．１とＮｏ．４とを比較すると、冷延累積圧下率が７
０％以上のＮｏ．１は、平均ｒ値が１．４以上となりプ
レス成形性が優れているのに対し、冷延累積圧下率が７
０％未満のＮｏ．４は、平均ｒ値が１．２と小さく、特
にタイプ２タンクへのプレス成形時に割れもしくはくび
れが発生した。From Table 2, it can be seen that No. 1 of the present invention example 1,3,3
It can be seen that Nos. 5 and 6 have excellent press formability and corrosion resistance and can be used as fuel tank materials for automobiles. Same steel A
No. using No. 1 and No. 750 ° C
The finish annealed No. 1 is 36% of total growth,
While the press formability was excellent, the finish annealed at less than 750 ° C. Sample No. 2 had a total elongation of only 13%, and cracks occurred during press molding into a fuel tank. Similarly, N
o. 1 and No. Compared with No. 4, the cold rolling cumulative rolling reduction is 7
No. 0% or more. The sample No. 1 has an average r value of 1.4 or more and has excellent press formability, while the cold rolling cumulative rolling reduction is 7%.
No. less than 0%. In No. 4, the average r value was as small as 1.2, and cracks or constrictions occurred particularly during press molding into a type 2 tank.
【００２６】Ｃｒ含有量が１０．５％未満の鋼Ｃを用い
たＮｏ．８は、要求される耐食性が得られていない。ま
たＣｒ含有量が１２％を超える鋼Ｄを用いたＮｏ．９、
Ｃ含有量が０．０１５％を超える鋼Ｅを用いたＮｏ．１
０，１１，１２、Ｎ含有量が０．０１％を超える鋼Ｆを
用いたＮｏ．１３，１４、Ｔｉ＋Ｎｂ含有量がＣ＋Ｎの
８倍未満である鋼Ｇを用いたＮｏ．１５については、全
伸びが３２％未満、場合によってはさらに平均ｒ値が
１．４未満となり、燃料タンクへのプレス成形時に割れ
やくびれが発生してしまう。[0026] No. 1 using steel C having a Cr content of less than 10.5%. No. 8 does not have the required corrosion resistance. In addition, No. 1 using steel D having a Cr content of more than 12%. 9,
No. 3 using steel E having a C content of more than 0.015%. 1
No. 0, 11, 12, and No. 3 using steel F having an N content exceeding 0.01%. Nos. 13, 14, No. 1 using steel G having a Ti + Nb content of less than 8 times that of C + N. For No. 15, the total elongation is less than 32%, and in some cases, the average r value is less than 1.4, and cracks and constrictions occur during press molding into a fuel tank.
【００２７】[0027]
【発明の効果】以上に説明した通り、本発明により複雑
な形状にプレス成形可能であり、さらに長期間にわたり
塩害環境や燃料による腐食に耐え得る自動車の燃料タン
ク用材として適用可能な溶融めっきフェライト系ステン
レス薄鋼板およびその製造方法を提供することが可能と
なったので、産業上の価値は極めて高い。As described above, according to the present invention, a hot-dip ferrite system which can be press-formed into a complex shape and which can be used as a material for a fuel tank of an automobile capable of withstanding a salt damage environment or corrosion by fuel for a long period of time. Since it has become possible to provide a stainless steel sheet and a method for producing the same, the industrial value is extremely high.
【図１】実験室で製作したＣｒ：１０．８％、Ｃ：０．
００４％、Ｎ：０．００６％、Ｔｉ：０．１５％を含有
し、板厚が０．８mmのフェライト系ステンレス冷延鋼板
の仕上焼鈍温度を変化させ、仕上焼鈍後にＡｌを主成分
とする溶融めっきを施した溶融めっき鋼板の全伸びを測
定した結果を示す図である。FIG. 1: Cr produced in a laboratory: 10.8%, C: 0.
The final annealing temperature of a ferritic stainless steel cold-rolled steel sheet containing 004%, N: 0.006%, Ti: 0.15% and having a thickness of 0.8 mm is changed, and after the final annealing, Al is the main component. It is a figure which shows the result of having measured the total elongation of the hot-dip-coated steel plate which performed hot-dip plating.
【図２】実験室で製作したＣｒ：１０．８％、Ｃ：０．
００４％、Ｎ：０．００６％、Ｔｉ：０．１５％を含有
するフェライト系ステンレス熱延鋼板を累積圧下率を変
化させて冷延した後に仕上焼鈍し、さらにＡｌを主成分
とする溶融めっきを施した溶融めっき鋼板の平均ｒ値を
測定した結果を示す図である。FIG. 2: Cr produced in a laboratory: 10.8%, C: 0.
A hot-rolled ferritic stainless steel sheet containing 004%, N: 0.006%, and Ti: 0.15% is cold-rolled by changing the cumulative rolling reduction, then finish-annealed, and then hot-dip plating mainly containing Al. It is a figure showing the result of having measured the average r value of the hot-dip-galvanized steel plate which gave.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 坂本 俊治 北九州市戸畑区飛幡町１−１ 新日本製鐵 株式会社八幡製鐵所内 (72)発明者 加藤 勝彦 北九州市戸畑区飛幡町１−１ 新日本製鐵 株式会社八幡製鐵所内 Ｆターム(参考） 4K037 EA04 EA12 EA18 EA19 EA31 EB03 FG03 FJ05 FJ06 FJ07 GA05 ──────────────────────────────────────────────────続 き Continuing on the front page (72) Inventor Shunji Sakamoto 1-1 Tobata-cho, Tobata-ku, Kitakyushu Nippon Steel Corporation Yawata Works (72) Inventor Katsuhiko Kato 1-1, Tobata-cho, Tobata-ku, Kitakyushu New Nippon Steel Corporation Yawata Works F-term (reference) 4K037 EA04 EA12 EA18 EA19 EA31 EB03 FG03 FJ05 FJ06 FJ07 GA05
Claims (3)
＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス鋼板をめっきの原板とし、
伸びが３２％以上、平均ｒ値が１．４以上であることを
特徴とする燃料タンク用溶融めっきフェライト系ステン
レス鋼板。1. A mass% of Cr: 10.5 to 12%, C ≦ 0.015%, N ≦ 0.01%, and one or two of Ti and Nb are (Ti + Nb) / (C
+ N) ≧ 8, the balance being Fe and stainless steel sheet composed of Fe and unavoidable impurities as the base sheet for plating,
A hot-dip ferritic stainless steel sheet for a fuel tank, having an elongation of at least 32% and an average r value of at least 1.4.
＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス冷延鋼板を、７５０℃以上
で仕上焼鈍した後に溶融めっきを施すことを特徴とする
燃料タンク用溶融めっきフェライト系ステンレス鋼板の
製造方法。2. In mass%, Cr: 10.5 to 12%, C ≦ 0.015%, N ≦ 0.01%, one or two of Ti and Nb are (Ti + Nb) / (C
Hot-dip ferrite for fuel tanks, comprising: subjecting a cold rolled ferritic stainless steel sheet containing in the range of + N) ≧ 8 and the balance consisting of Fe and unavoidable impurities to finish-annealing at 750 ° C. or higher and then hot-dip coating. For producing stainless steel sheet.
＋Ｎ）≧８ の範囲で含有し、残部がＦｅおよび不可避的不純物から
なるフェライト系ステンレス熱延鋼板を、累積圧下率７
０％以上で冷間圧延し、さらに仕上焼鈍した後に溶融め
っきを施すことを特徴とする燃料タンク用溶融めっきフ
ェライト系ステンレス鋼板の製造方法。3. In mass%, Cr: 10.5 to 12%, C ≦ 0.015%, N ≦ 0.01%, one or two of Ti and Nb are (Ti + Nb) / (C
+ N) ≧ 8, the balance being Fe and unavoidable impurities.
A method for producing a hot-dip ferritic stainless steel sheet for a fuel tank, wherein the hot-rolled ferritic stainless steel sheet for a fuel tank is cold-rolled at 0% or more, and further subjected to finish annealing and then hot-dip plating.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000282978A JP2002097552A (en) | 2000-09-19 | 2000-09-19 | Hot-dip plated ferritic stainless-steel sheet for fuel tank and manufacturing method therefor |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2000282978A JP2002097552A (en) | 2000-09-19 | 2000-09-19 | Hot-dip plated ferritic stainless-steel sheet for fuel tank and manufacturing method therefor |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2002097552A true JP2002097552A (en) | 2002-04-02 |
Family
ID=18767399
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
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| Country | Link |
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| JP (1) | JP2002097552A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008062650A1 (en) * | 2006-11-21 | 2008-05-29 | Nippon Steel & Sumikin Stainless Steel Corporation | Surface-treated stainless-steel sheet excellent in salt damage/corrosion resistance and weld reliability for automotive fuel tank and for automotive fuel pipe and surface-treated stainless-steel welded pipe with excellent suitability for pipe expansion processing for automotive petrol pipe |
| WO2019045188A1 (en) * | 2017-08-31 | 2019-03-07 | 주식회사 포스코 | Ferrite-based stainless steel having improved heat radiation property and processability and method for preparing same |
| US11427881B2 (en) | 2014-10-31 | 2022-08-30 | Nippon Steel Stainless Steel Corporation | Ferrite-based stainless steel plate, steel pipe, and production method therefor |
-
2000
- 2000-09-19 JP JP2000282978A patent/JP2002097552A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2008062650A1 (en) * | 2006-11-21 | 2008-05-29 | Nippon Steel & Sumikin Stainless Steel Corporation | Surface-treated stainless-steel sheet excellent in salt damage/corrosion resistance and weld reliability for automotive fuel tank and for automotive fuel pipe and surface-treated stainless-steel welded pipe with excellent suitability for pipe expansion processing for automotive petrol pipe |
| JP2009068102A (en) * | 2006-11-21 | 2009-04-02 | Nippon Steel & Sumikin Stainless Steel Corp | Surface-treated stainless steel sheet having excellent salt corrosion resistance and weld zone reliability for automotive fuel tank and automobile fuel pipe, and welded pipe excellent in pipe expandability made from surface-treated stainless steel for automobile fuel inlet pipe |
| US11427881B2 (en) | 2014-10-31 | 2022-08-30 | Nippon Steel Stainless Steel Corporation | Ferrite-based stainless steel plate, steel pipe, and production method therefor |
| WO2019045188A1 (en) * | 2017-08-31 | 2019-03-07 | 주식회사 포스코 | Ferrite-based stainless steel having improved heat radiation property and processability and method for preparing same |
| KR20190024137A (en) * | 2017-08-31 | 2019-03-08 | 주식회사 포스코 | Ferritic stainless steel with improved heat dissipation and workability and method of manufacturing the same |
| KR101964318B1 (en) * | 2017-08-31 | 2019-04-01 | 주식회사포스코 | Ferritic stainless steel with improved heat dissipation and workability and method of manufacturing the same |
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