JP2016060945A - MOLTEN Al-BASED PLATED SHEET STEEL - Google Patents
MOLTEN Al-BASED PLATED SHEET STEEL Download PDFInfo
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- JP2016060945A JP2016060945A JP2014190406A JP2014190406A JP2016060945A JP 2016060945 A JP2016060945 A JP 2016060945A JP 2014190406 A JP2014190406 A JP 2014190406A JP 2014190406 A JP2014190406 A JP 2014190406A JP 2016060945 A JP2016060945 A JP 2016060945A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 95
- 239000010959 steel Substances 0.000 title claims abstract description 95
- 238000007747 plating Methods 0.000 claims description 91
- 229910001335 Galvanized steel Inorganic materials 0.000 claims description 2
- 239000008397 galvanized steel Substances 0.000 claims description 2
- 230000007797 corrosion Effects 0.000 abstract description 68
- 238000005260 corrosion Methods 0.000 abstract description 68
- 238000004519 manufacturing process Methods 0.000 abstract description 3
- 239000002184 metal Substances 0.000 abstract description 2
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000011248 coating agent Substances 0.000 description 60
- 238000000576 coating method Methods 0.000 description 60
- 229910045601 alloy Inorganic materials 0.000 description 16
- 239000000956 alloy Substances 0.000 description 16
- 239000000203 mixture Substances 0.000 description 16
- 238000011156 evaluation Methods 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 239000000126 substance Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 239000004566 building material Substances 0.000 description 6
- 239000000047 product Substances 0.000 description 6
- 230000008961 swelling Effects 0.000 description 6
- 238000006243 chemical reaction Methods 0.000 description 5
- 238000004070 electrodeposition Methods 0.000 description 5
- 239000012535 impurity Substances 0.000 description 5
- 238000010422 painting Methods 0.000 description 5
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 4
- 150000001875 compounds Chemical class 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000000034 method Methods 0.000 description 4
- 229910018191 Al—Fe—Si Inorganic materials 0.000 description 3
- 230000001133 acceleration Effects 0.000 description 3
- 239000003795 chemical substances by application Substances 0.000 description 3
- 229910000765 intermetallic Inorganic materials 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000012545 processing Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 239000013585 weight reducing agent Substances 0.000 description 3
- LRXTYHSAJDENHV-UHFFFAOYSA-H zinc phosphate Chemical compound [Zn+2].[Zn+2].[Zn+2].[O-]P([O-])([O-])=O.[O-]P([O-])([O-])=O LRXTYHSAJDENHV-UHFFFAOYSA-H 0.000 description 3
- 229910000165 zinc phosphate Inorganic materials 0.000 description 3
- 229910018125 Al-Si Inorganic materials 0.000 description 2
- 229910018520 Al—Si Inorganic materials 0.000 description 2
- 239000007864 aqueous solution Substances 0.000 description 2
- 210000004027 cell Anatomy 0.000 description 2
- 239000010960 cold rolled steel Substances 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 239000003973 paint Substances 0.000 description 2
- 238000004611 spectroscopical analysis Methods 0.000 description 2
- 238000005507 spraying Methods 0.000 description 2
- 230000006641 stabilisation Effects 0.000 description 2
- 238000011105 stabilization Methods 0.000 description 2
- 239000011701 zinc Substances 0.000 description 2
- 229910018072 Al 2 O 3 Inorganic materials 0.000 description 1
- 229910000838 Al alloy Inorganic materials 0.000 description 1
- -1 Mg 2 Si Chemical class 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
- 229910019021 Mg 2 Sn Inorganic materials 0.000 description 1
- 229910017706 MgZn Inorganic materials 0.000 description 1
- 238000010521 absorption reaction Methods 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 238000005452 bending Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 230000000052 comparative effect Effects 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000003750 conditioning effect Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000007796 conventional method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 210000001787 dendrite Anatomy 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 239000005002 finish coating Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000002828 fuel tank Substances 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 239000002210 silicon-based material Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000001629 suppression Effects 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 238000010792 warming Methods 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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Abstract
Description
本発明は、塗装後耐食性に優れた溶融Ａｌ系めっき鋼板に関するものである。 The present invention relates to a hot-dip Al-based plated steel sheet having excellent post-coating corrosion resistance.
溶融Ａｌ系めっき鋼板は、通常の溶融Ｚｎめっき鋼板と比較して、耐食性及び耐熱性に優れる。
一般的に、溶融Ａｌ系めっき鋼板は、鋼スラブを熱間圧延若しくは冷間圧延した薄鋼板を下地鋼板として用い、該下地鋼板を連続式溶融めっきラインの焼鈍炉にて再結晶焼鈍及び溶融めっき処理を行うことによって製造される。この形成されたＡｌ系めっき層は、下地鋼板との界面に存在する合金層と、その上に存在する上層とを備えている。さらに、上層は、主としてＡｌがめっき皮膜の膜厚方向に積層するようにデンドライト凝固した部分（α−Ａｌ相）と、残りのインターデンドライトの部分からなり、インターデンドライトの一部には、後述するＦｅやＳｉなどの金属間化合物や単体が存在する。この上層の特徴的な皮膜構造により、表面からの腐食進行経路が複雑になり腐食が容易に下地鋼板に到達しにくくなるため、溶融Ａｌ系めっき鋼板は、優れた耐食性を有することが可能である。
さらに、めっきの主成分であるＡｌは、本来熱力学的には活性な金属であるが、大気中などの有酸素雰囲気では表面に酸化膜を形成し、この酸化膜の安定性に起因して優れた耐食性を有する。
The hot-dip Al-based plated steel sheet is excellent in corrosion resistance and heat resistance as compared with a normal hot-dip Zn-plated steel sheet.
In general, hot-dip Al-based plated steel sheets use thin steel sheets obtained by hot-rolling or cold-rolling steel slabs as base steel sheets, and the base steel sheets are recrystallized and hot-dip plated in an annealing furnace of a continuous hot-dip plating line. Manufactured by processing. The formed Al-based plating layer includes an alloy layer present at the interface with the base steel plate and an upper layer present thereon. Furthermore, the upper layer mainly comprises a dendrite solidified portion (α-Al phase) so that Al is laminated in the film thickness direction of the plating film and the remaining interdendritic portion. There are intermetallic compounds and simple substances such as Fe and Si. The characteristic coating structure of this upper layer complicates the corrosion progression path from the surface and makes it difficult for the corrosion to reach the underlying steel sheet. Therefore, the molten Al-based plated steel sheet can have excellent corrosion resistance. .
In addition, Al, which is the main component of plating, is originally a thermodynamically active metal, but an oxide film is formed on the surface in an aerobic atmosphere such as in the atmosphere, and this is due to the stability of this oxide film. Excellent corrosion resistance.
なお、めっき浴には、不可避的不純物、鋼板やめっき浴中の機器等から溶出するＦｅが含まれており、その他、過度の合金層成長を抑制するためのＳｉが通常添加される。このＳｉは合金層に金属間化合物の形、あるいは上層に金属間化合物、固溶体若しくは単体の形で存在している。そして、このＳｉの働きにより、溶融Ａｌ系めっき鋼板の界面の合金層成長が抑えられ、合金層厚さは約１〜５μｍ程度となっている。めっき層厚が同一ならば、合金層が薄いほど耐食性向上に効果のある上層が厚くなるので、合金層の成長を抑制することは耐食性の向上に寄与することになる。また、合金層は上層よりも固く、加工時にクラックの起点として作用することから、合金層の成長抑制はクラックの発生を減少させ、曲げ加工性を向上させる効果をもたらすことにもなる。そして、発生したクラック部は下地鋼板が露出しており耐食性に劣るので、合金層の成長を抑制し、クラックの発生を抑制することは曲げ加工部耐食性をも向上させることになる。 Note that the plating bath contains inevitable impurities, Fe eluted from steel plates, equipment in the plating bath, and the like, and in addition, Si for suppressing excessive alloy layer growth is usually added. This Si is present in the form of an intermetallic compound in the alloy layer, or in the form of an intermetallic compound, solid solution or simple substance in the upper layer. And, by the action of Si, the growth of the alloy layer at the interface of the molten Al-based plated steel sheet is suppressed, and the alloy layer thickness is about 1 to 5 μm. If the plating layer thickness is the same, the thinner the alloy layer, the thicker the upper layer that is effective for improving the corrosion resistance. Therefore, suppressing the growth of the alloy layer contributes to the improvement of the corrosion resistance. In addition, since the alloy layer is harder than the upper layer and acts as a starting point of cracks during processing, the suppression of the growth of the alloy layer also reduces the occurrence of cracks and brings about the effect of improving bending workability. And since the base steel plate is exposed and the generated crack portion is inferior in corrosion resistance, suppressing the growth of the alloy layer and suppressing the generation of cracks also improves the corrosion resistance of the bent portion.
このように耐食性に優れる溶融Ａｌ系めっき鋼板は、長期間屋外に曝される屋根や壁などの建材分野を中心に需要が伸び、近年は、自動車分野においても、優れた耐熱性を活かしてマフラー、燃料タンクなどの特定部品で使用されている。特に、自動車分野においては、地球温暖化対策の一環で車体を軽量化して燃費を向上させＣＯ2排出量を削減することが求められている。このため、現在、高強度鋼板の使用による軽量化と、鋼板の耐食性向上によるゲージダウンが強く望まれている。 The demand for molten Al-based plated steel sheets with excellent corrosion resistance has increased in the field of building materials such as roofs and walls that have been exposed to the outdoors for long periods of time. Used in specific parts such as fuel tanks. In particular, in the automobile field, as a part of global warming countermeasures, it is required to reduce the CO 2 emission by reducing the weight of the vehicle body and improving the fuel consumption. For this reason, at present, there is a strong demand for weight reduction by using a high-strength steel plate and gauge down by improving the corrosion resistance of the steel plate.
しかしながら、溶融Ａｌ系めっき鋼板を自動車分野、特に外板パネルに用いようとした場合には、次の問題があった。
溶融Ａｌ系めっき鋼板を自動車外板パネルとして使用する場合、該めっき鋼板は連続式溶融めっき設備でめっきまで施した状態で自動車メーカー等に供される。そこでパネル部品形状に加工された後に化成処理、さらに電着塗装、中塗り塗装、上塗り塗装の自動車用３コート塗装が施されることが一般的である。ただし、溶融Ａｌ系めっき鋼板を用いた外板パネルは、塗膜に損傷が生じた際に傷部からの塗膜膨れが生じ易いという問題があった。
塗装後腐食の一つである塗膜膨れは、下地鋼板が露出する傷部がカソード、腐食先端部がアノード、腐食最先端部がカソードのような塗膜下で局部電池を形成するために起こる事象である。Ａｌ系めっき鋼板は、めっき層中のインターデンドライトに形成した針状のＳｉやＡｌ−Ｆｅ−Ｓｉ化合物がいずれもＡｌよりも貴な電位を示し、局部的にカソードサイトとして働くため、塗膜下で局部電池を形成する。これにより、傷部を起点にインターデンドライトの選択腐食が塗膜／めっき界面で発生する。これが進行して大きな塗膜膨れを起こす結果、十分な塗装後耐食性を確保できなくなる。
However, when trying to use the molten Al-based plated steel sheet in the automotive field, particularly in the outer panel, there are the following problems.
When a hot-dip Al-based plated steel sheet is used as an automobile outer panel, the plated steel sheet is supplied to an automobile manufacturer or the like in a state where it has been plated up with a continuous hot-dip plating facility. Therefore, after processing into a panel part shape, chemical conversion treatment, and further three-coat coating for automobiles of electrodeposition coating, intermediate coating, and top coating are generally performed. However, the outer panel using the molten Al-based plated steel sheet has a problem that the coating film swells easily from the scratch when the coating film is damaged.
Swelling of the coating film, which is one type of post-coating corrosion, occurs because a damaged cell where the underlying steel plate is exposed forms a local cell under the coating film, such as the cathode, the corrosion tip is the anode, and the corrosion tip is the cathode. It is an event. The Al-based plated steel sheet has needle-like Si and Al-Fe-Si compounds formed on the interdendrite in the plating layer, both of which have a higher potential than Al and locally act as cathode sites. To form a local battery. As a result, selective corrosion of the interdendrite occurs at the coating film / plating interface starting from the scratch. As a result of this progressing and causing large swelling of the coating film, sufficient post-coating corrosion resistance cannot be ensured.
一方、溶融Ａｌ系めっき鋼板を建屋の屋根材や壁材として建材分野で用いた場合もまた、塗装後耐食性が問題となっている。屋根材や壁材として使用される場合は、溶融めっき鋼板は一般的に下塗り塗装、上塗り塗装を施した状態で建築会社等に供され、必要なサイズに剪断してから使用される。このため、必然的に塗装がされていない鋼板端面が露出する。ここを起点にエッジクリープと呼ばれる塗膜膨れが発生することがある。溶融Ａｌ系めっき鋼板を建材分野で用いた場合、自動車外板パネルの場合と同様に、鋼板端面部を起点に塗膜／めっき界面におけるインターデンドライトの選択腐食が起こる。この結果、溶融Ｚｎめっきに比べて著しく大きなエッジクリープを生じて塗装後耐食性が劣ることがあった。 On the other hand, when the molten Al-based plated steel sheet is used in the building material field as a roofing material or wall material of a building, corrosion resistance after painting is also a problem. When used as a roofing material or a wall material, a hot-dip plated steel sheet is generally provided to a construction company or the like in a state where a base coat or top coat is applied, and is used after being sheared to a required size. For this reason, the steel plate end surface which is not necessarily coated is exposed. From this point, a swollen coating called edge creep may occur. When a hot-dip Al-based plated steel sheet is used in the building material field, selective corrosion of interdrite occurs at the coating film / plating interface starting from the end face of the steel sheet, as in the case of an automobile outer panel. As a result, the edge creep may be significantly larger than that of hot-dip Zn plating, resulting in inferior post-coating corrosion resistance.
上記問題を解決すべく、例えば特許文献１には、めっき組成にＭｇ、又はさらにＳｎ等を添加し、めっき層中にＭｇ2Ｓｉ、ＭｇＺｎ2 、Ｍｇ2Ｓｎ等のＭｇ化合物を形成させることで、鋼板端面からの赤錆発生を改善した溶融Ａｌ系めっき鋼板が開示されている。
しかしながら、特許文献１に開示される溶融Ａｌ系めっき鋼板に塗装を施した場合、塗装後の塗膜に損傷が生じたときの耐食性（塗装後耐食性）は、依然として解消できていなかった。
In order to solve the above problem, for example, in Patent Document 1, Mg or Sn is further added to the plating composition, and Mg compounds such as Mg 2 Si, MgZn 2 and Mg 2 Sn are formed in the plating layer. A hot-dip Al-based plated steel sheet that has improved the occurrence of red rust from the end face of the steel sheet is disclosed.
However, when coating was performed on the molten Al-based plated steel sheet disclosed in Patent Document 1, the corrosion resistance (corrosion resistance after coating) when the coated film after the coating was damaged could not be eliminated.
また、溶融Ａｌ系めっき鋼板は、建材や家電分野に塗装を施さず使用される場合もある。なかでも、壁材や家電製品の背面板等に使用される場合には、めっき鋼板の表面が人目に曝されることになるので、高い外観品位が求められる。外観品位とは、主に、異物付着や不めっき、傷等の欠陥有無の他に、模様や色調のムラのないことをいう。後者の模様や色調については、溶融Ａｌ系めっき鋼板が無塗装で使用される場合により強く求められる品位である。そのため、塗装鋼板として使用する溶融Ａｌ系めっき鋼板の全てが、無塗装で用いられる用途（壁材、家電製品の背面板等）に適用できるわけではなく、外観品位のさらなる向上についても望まれていた。
さらに、溶融Ａｌ系めっき鋼板の場合、めっきの成分組成によって、めっき後の表面が徐々に黒色に変化（黒変）することがあった。例えば、特許文献１に示されたＳｎを添加した溶融Ａｌ系めっき鋼板でも、黒変が発生する場合がある。このように、無塗装で使用する用途に全ての溶融Ａｌ系めっき鋼板を適用することができないという問題があった。
Further, the molten Al-based plated steel sheet may be used without being applied in the building materials and home appliance fields. Especially, when it is used for a wall material, a back plate of home appliances, and the like, the surface of the plated steel sheet is exposed to the human eye, so a high appearance quality is required. The appearance quality mainly means that there is no unevenness in the pattern and color tone in addition to the presence or absence of foreign matter adhesion, non-plating, scratches and the like. About the latter pattern and color tone, it is a grade strongly requested | required by the case where a fusion | melting Al system plating steel plate is used without coating. For this reason, not all of the molten Al-based plated steel sheets used as coated steel sheets can be applied to non-painting applications (wall materials, back plates of household electrical appliances, etc.), and further improvement in appearance quality is also desired. It was.
Furthermore, in the case of a hot-dip Al-based plated steel sheet, the surface after plating may gradually change to black (blackening) depending on the component composition of plating. For example, blackening may occur even in a hot-dip Al-based plated steel sheet to which Sn shown in Patent Document 1 is added. Thus, there existed a problem that not all the hot-dip Al type plated steel sheets could be applied to the use used without coating.
本発明は、かかる事情に鑑みてなされたものであって、優れた塗装後耐食性を有する溶融Ａｌ系めっき鋼板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 hot-dip Al type plated steel plate which has the outstanding post-coating corrosion resistance.
本発明者らは、上記の課題を解決すべく、鋭意研究を重ねた。その結果、Ａｌ系めっき層中に、特定量のＳｎを含有させることにより、従来にない優れた塗装後耐食性が得られることを見出した。 The inventors of the present invention have made extensive studies to solve the above problems. As a result, it has been found that by including a specific amount of Sn in the Al-based plating layer, excellent post-coating corrosion resistance, which has not been conventionally achieved, can be obtained.
本発明は、上記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］Ｓｎを０．０１〜１０質量％含有するめっき層を有することを特徴とする溶融Ａｌ系めっき鋼板。
The present invention has been made based on the above findings, and the gist thereof is as follows.
[1] A hot-dip Al-based plated steel sheet having a plating layer containing 0.01 to 10% by mass of Sn.
［２］前記めっき層が、さらにＭｇ及び／又はＣａを、合計で０．０１〜１０質量％含有することを特徴とする上記［１］に記載の溶融Ａｌ系めっき鋼板。 [2] The molten Al-based plated steel sheet according to [1], wherein the plating layer further contains 0.01 to 10% by mass of Mg and / or Ca in total.
［３］前記めっき層が、さらに、Ｓｉを０．１〜１０質量％含有することを特徴とする上記［１］又は［２］に記載の溶融Ａｌ系めっき鋼板。 [3] The hot-dip galvanized steel sheet according to [1] or [2], wherein the plating layer further contains 0.1 to 10% by mass of Si.
［４］前記めっき層のＳｉ含有量が、３質量％以下であることを特徴とする上記［３］に記載の溶融Ａｌ系めっき鋼板。 [4] The hot-dip Al-based plated steel sheet according to the above [3], wherein the Si content of the plating layer is 3% by mass or less.
［５］前記めっき層のＳｉ含有量が、２質量％以下であることを特徴とする上記［４］に記載の溶融Ａｌ系めっき鋼板。 [5] The hot-dip Al-based plated steel sheet according to [4], wherein the plating layer has an Si content of 2% by mass or less.
［６］前記めっき層のＳｎ含有量が、１質量％以下であることを特徴とする上記［１］〜［５］のいずれかに記載の溶融Ａｌ系めっき鋼板。 [6] The hot-dip Al-based plated steel sheet according to any one of [1] to [5], wherein the plating layer has an Sn content of 1% by mass or less.
［７］前記めっき層のＡｌ含有量が、９０質量％を超えることを特徴とする上記［１］〜［６］のいずれかに記載の溶融Ａｌ系めっき鋼板。 [7] The molten Al-based plated steel sheet according to any one of [1] to [6], wherein the Al content of the plating layer exceeds 90% by mass.
本発明によれば、耐食性、特に塗装後耐食性に優れた溶融Ａｌ系めっき鋼板が得られる。そして、本発明の溶融Ａｌ系めっき鋼板を高強度鋼板とすることによって、自動車分野において、軽量化と優れた耐食性の両立が可能となる。また、建材分野で屋根材や壁材として使用することにより、建屋寿命の延命が可能となる。 According to the present invention, a hot-dip Al-based plated steel sheet having excellent corrosion resistance, particularly post-coating corrosion resistance can be obtained. And by making the hot-dip Al-based plated steel sheet of the present invention a high-strength steel sheet, it is possible to achieve both weight reduction and excellent corrosion resistance in the automotive field. In addition, the life of the building can be extended by using it as a roofing material or wall material in the building material field.
以下、本発明について具体的に説明する。尚、以下の説明において、めっき層、及びめっき浴の組成を示す各元素の含有量の単位はいずれも「質量％」であり、以下、特に断らない限り単に「％」で示す。 Hereinafter, the present invention will be specifically described. In the following description, the unit of the content of each element indicating the composition of the plating layer and the plating bath is “mass%”, and hereinafter, it is simply indicated by “%” unless otherwise specified.
先ず始めに、本発明で最も重要である、溶融Ａｌ系めっき鋼板による塗装後耐食性の改善方法について説明する。
本発明の溶融Ａｌ系めっき鋼板は、めっき層中に、Ａｌに加えて、Ｓｎ：０．０１〜１０％を含有することを特徴とする。めっき層中にＳｎを含有することで、本発明で課題とする塗装後耐食性の改善が可能となる。
First, a method for improving post-coating corrosion resistance using a hot-dip Al-based plated steel sheet, which is most important in the present invention, will be described.
The hot-dip Al-based plated steel sheet of the present invention is characterized by containing Sn: 0.01 to 10% in addition to Al in the plating layer. By containing Sn in the plating layer, it is possible to improve the post-coating corrosion resistance, which is a problem in the present invention.
めっき層中に特定量のＳｎを含まない、従来の溶融Ａｌ系めっき鋼板のめっき層が大気に触れると、α−Ａｌ相の周囲に緻密、且つ安定なＡｌ2Ｏ3の酸化膜が直ぐに形成される。この酸化膜による保護作用によってα−Ａｌ相の溶解性は低くなる。一方、インターデンドライトに形成した針状のＳｉやＡｌ−Ｆｅ−Ｓｉ化合物は、いずれもα−Ａｌ相よりも貴な電位を示し、局部的にカソードサイトとして働くため、塗膜下で局部電池を形成することになる。これにより、傷部を起点としたインターデンドライトの選択腐食が、塗膜／めっき界面で発生する。これが進行して大きな塗膜膨れを起こすことで、塗装後耐食性が低下することとなる。
ここで、塗装鋼板の下地として、Ｓｎを含有した溶融Ａｌ系めっき鋼板を用いた場合には、Ｓｎが、上述したα−Ａｌ相の周囲に形成するＡｌ酸化膜を破壊し、α−Ａｌ相の溶解性を上げる。これによって、α−Ａｌ相の均一腐食が可能となり、従来のＡｌ系めっき鋼板を下地に用いた場合に問題となるインターデンドライトの選択腐食を抑制できる。その結果、本発明の溶融Ａｌ系めっき鋼板は、優れた塗装後耐食性を示す。
When a plating layer of a conventional hot-dip Al-plated steel sheet that does not contain a specific amount of Sn in the plating layer is exposed to the atmosphere, a dense and stable Al 2 O 3 oxide film immediately forms around the α-Al phase. Is done. Due to the protective action of the oxide film, the solubility of the α-Al phase is lowered. On the other hand, the needle-like Si and Al-Fe-Si compounds formed on the interdendrite all have a higher potential than the α-Al phase and locally act as cathode sites. Will form. Thereby, selective corrosion of the interdendrite starting from the scratch occurs at the coating film / plating interface. As this progresses and causes a large swelling of the coating film, the corrosion resistance after coating is reduced.
Here, when a molten Al-based plated steel sheet containing Sn is used as the base of the coated steel sheet, Sn destroys the Al oxide film formed around the α-Al phase described above, and the α-Al phase Increase the solubility of. As a result, the α-Al phase can be uniformly corroded, and selective corrosion of the interdendrite, which is a problem when a conventional Al-based plated steel sheet is used as a base, can be suppressed. As a result, the molten Al-based plated steel sheet of the present invention exhibits excellent post-coating corrosion resistance.
次に、本発明の対象とする溶融Ａｌ系めっき鋼板のめっき層の組成について説明する。
前記めっき層中のＳｎ含有量を、０．０１〜１０％としたのは次の理由からである。それぞれ、Ｓｎが０．０１％未満の場合は、上記に示したインターデンドライトの選択腐食を抑制可能とするＡｌ酸化膜の破壊が起こらないため、塗装後耐食性の向上は望めない。逆に、Ｓｎが１０％を超える場合には、Ａｌ酸化膜の破壊が激しく起こり、めっき層全体の溶解性が過度に上昇する。その結果、めっき層を均一腐食させても、その溶解速度が大きくなる。このため、大きな膨れ幅を生じ、塗装後耐食性が劣化する。よって、優れた塗装後耐食性を安定的に得るためには、Ｓｎの含有量を０．０１〜１０％の範囲とする必要がある。
Next, the composition of the plating layer of the hot-dip Al-based plated steel sheet that is the subject of the present invention will be described.
The reason why the Sn content in the plating layer is set to 0.01 to 10% is as follows. In each case, when Sn is less than 0.01%, the Al oxide film capable of suppressing the selective corrosion of the interdendrite described above does not occur, so that improvement in corrosion resistance after painting cannot be expected. On the other hand, when Sn exceeds 10%, the Al oxide film is severely destroyed, and the solubility of the entire plating layer is excessively increased. As a result, even if the plating layer is uniformly corroded, the dissolution rate is increased. For this reason, a large swollen width is generated, and the corrosion resistance after coating is deteriorated. Therefore, in order to stably obtain excellent post-coating corrosion resistance, the Sn content needs to be in the range of 0.01 to 10%.
また、前記めっき層中のＳｎ含有量は、０．１％以下とすることで、めっき表面が黒色化することがなく、外観品位に優れる。さらに、１％以下であれば塗装を施さず使用する場合でも表面外観が問題となることがない。そのため、塗装後耐食性と優れためっき外観とを両立する観点からは、前記めっき層中のＳｎ含有量を、０．０１〜１％とすることが好ましく、０．０１％〜０．１％とすることがより好ましい。 Moreover, Sn content in the said plating layer shall be 0.1% or less, and it does not blacken the plating surface but is excellent in appearance quality. Furthermore, if it is 1% or less, the surface appearance does not become a problem even when it is used without being coated. Therefore, from the viewpoint of achieving both corrosion resistance after coating and excellent plating appearance, the Sn content in the plating layer is preferably 0.01 to 1%, and 0.01% to 0.1%. More preferably.
さらに、前記めっき層は、Ｍｇ及び／又はＣａを、合計で０．０１〜１０％含有することが好ましい。Ｍｇ及びＣａは、腐食により生成した腐食生成物中に取り込まれることで、腐食生成物の安定化を図り、鋼板の腐食進行を早期に抑えることができる。Ｍｇ及び／又はＣａの合計含有量を０．０１％以上としたのは、前記腐食生成物に取り込まれるＭｇやＣａの量を十分に確保でき、腐食生成物の安定化を望めるためである。また、前記含有量を１０％以下としたのは、腐食生成物の安定化効果を確保しつつ、製造コストの上昇を抑えることができるからである。 Furthermore, the plating layer preferably contains 0.01 to 10% of Mg and / or Ca in total. Mg and Ca are taken into the corrosion product generated by the corrosion, so that the corrosion product can be stabilized and the corrosion of the steel sheet can be suppressed at an early stage. The reason why the total content of Mg and / or Ca is set to 0.01% or more is that a sufficient amount of Mg and Ca taken into the corrosion product can be secured and the corrosion product can be stabilized. The reason why the content is set to 10% or less is that an increase in manufacturing cost can be suppressed while securing the stabilization effect of the corrosion product.
また、前記めっき層中の、Ｍｇ及び／又はＣａの合計含有量は、めっき浴中の成分管理によって調整される。なお、めっき浴中のＭｇ及び／又はＣａの含有量が３％を超えるとドロスの生成量が多くなり、成分管理が難しくなるといった問題が生じる。よって、めっき浴の組成管理の観点からは、前記含有量を０．０１〜５％の範囲とすることが好ましく、０．０１〜３％の範囲とすることがより好ましい。 Moreover, the total content of Mg and / or Ca in the plating layer is adjusted by component management in the plating bath. In addition, when the content of Mg and / or Ca in the plating bath exceeds 3%, there is a problem that the amount of dross generated increases and component management becomes difficult. Therefore, from the viewpoint of composition management of the plating bath, the content is preferably in the range of 0.01 to 5%, and more preferably in the range of 0.01 to 3%.
なお、前記めっき層中にＭｇとＣａを複合で含有する場合も、単独で含有する場合と同じ効果が得られるが、実際の操業の点から、めっき浴組成を安定かつ容易に管理するべく、含有させる元素数を少なくすること、具体的には、Ｍｇ又はＣａを単独で含有させることが好ましい。 In addition, in the case where Mg and Ca are contained in a composite in the plating layer, the same effect as the case of containing alone can be obtained, but in terms of actual operation, in order to manage the plating bath composition stably and easily, It is preferable to reduce the number of elements to be contained, specifically, to contain Mg or Ca alone.
さらに、本発明の溶融Ａｌ系めっき鋼板は、前記めっき層中にＳｉを０．１〜１０％含有することが好ましい。Ｓｉは、下地鋼板との界面に形成する界面合金層の成長を抑制し、耐食性や加工性の向上を目的にめっき浴中に添加され、めっき層に含有される。具体的には、溶融Ａｌ系めっき鋼板の場合、Ｓｉを含有させためっき浴中に鋼板を浸漬すると、鋼板表面のＦｅと浴中のＡｌやＳｉが合金化反応し、Ｆｅ-Ａｌ系及び／又はＦｅ−Ａｌ−Ｓｉ系の化合物を形成する。このＦｅ-Ａｌ系及び／又はＦｅ−Ａｌ−Ｓｉ系界面合金層の形成により、界面合金層の成長が抑制される。そして、めっき浴中のＳｉ含有量は、０．１％以上とすることで界面合金層の十分な成長抑制が可能となる。
なお、界面合金層に取り込まれない余剰のＳｉはめっき上層のインターデンドライトに単体又はＡｌ-Ｆｅ-Ｓｉなどの化合物として析出する。これらは前述のとおり、いずれもα−Ａｌ相よりも貴な電位を示し、局部的にカソードサイトとして働くため、インターデンドライトの選択腐食を引き起こす。この選択腐食を抑制するためには、可能な限り余剰のＳｉ量を減らすことが必要であり、めっき浴中のＳｉ含有量を３％以下にすることが好ましい。２％以下にすることがより好ましい。よって、めっき浴中のＳｉ含有量の好適範囲は、０．１〜１０％であり、より好ましい範囲は０．１〜３％、さらに好ましい範囲は０．１〜２％である。Ａｌ系めっき鋼板の場合、めっき層の組成がめっき浴組成とほぼ同等となるため、めっき層中のＳｉ含有量の好適範囲はめっき浴中のＳｉ含有量の好適範囲と同等の０．１〜１０％であり、より好ましい範囲は０．１〜３％、さらに好ましい範囲は０．１〜２％である。
Furthermore, the molten Al-based plated steel sheet of the present invention preferably contains 0.1 to 10% of Si in the plating layer. Si is added to the plating bath for the purpose of suppressing the growth of the interfacial alloy layer formed at the interface with the base steel sheet and improving corrosion resistance and workability, and is contained in the plating layer. Specifically, in the case of a hot-dip Al-based plated steel sheet, when the steel sheet is immersed in a plating bath containing Si, Fe on the steel sheet surface reacts with Al or Si in the bath to form an Fe-Al based and / or Alternatively, an Fe—Al—Si based compound is formed. The formation of the Fe—Al-based and / or Fe—Al—Si-based interface alloy layer suppresses the growth of the interface alloy layer. And the Si content in the plating bath can be 0.1% or more, and the growth of the interface alloy layer can be sufficiently suppressed.
Excess Si that is not taken into the interface alloy layer precipitates as a single substance or a compound such as Al—Fe—Si on the interdrite of the plating upper layer. As described above, these all show a higher potential than the α-Al phase and locally act as cathode sites, thus causing selective corrosion of the interdendrite. In order to suppress this selective corrosion, it is necessary to reduce the surplus Si amount as much as possible, and it is preferable to make the Si content in the plating bath 3% or less. It is more preferable to make it 2% or less. Therefore, the preferable range of the Si content in the plating bath is 0.1 to 10%, the more preferable range is 0.1 to 3%, and the further preferable range is 0.1 to 2%. In the case of an Al-based plated steel sheet, since the composition of the plating layer is almost equivalent to the plating bath composition, the preferred range of the Si content in the plating layer is 0.1 to the same preferred range of the Si content in the plating bath. 10%, a more preferable range is 0.1 to 3%, and a further preferable range is 0.1 to 2%.
本発明の溶融Ａｌ系めっき鋼板のめっき層は、Ａｌを主成分としており、より優れた耐食性及び耐熱性を確保する観点から、好ましくは９０％超え、より好ましくは９５％超えの含有量で含有する。なお、めっき層中には、鋼板やめっき浴中の機器等から溶出するＦｅや、Ａｌ合金原料中に含有した不可避的不純物が含まれる。不可避的不純物の種類としては、例えば、Ｃｒ、Ｃｕ、Ｍｏ、Ｎｉ、Ｔｉ、Ｚｒ等が挙げられる。前記、Ｆｅ及び不可避的不純物の総含有量は特に限定はしないが、めっき層の耐食性と均一な溶解性を維持するという観点から、１％以下であることが好ましい。
なお、前記めっき層は、溶融Ａｌ系のめっきであり、Ｚｎについては、不可避的不純物である場合を除いて含有しない。
The plating layer of the hot-dip Al-based plated steel sheet of the present invention contains Al as a main component, and is preferably contained in a content exceeding 90%, more preferably exceeding 95%, from the viewpoint of ensuring better corrosion resistance and heat resistance. To do. In addition, in the plating layer, inevitable impurities contained in Fe eluting from the steel plate, the equipment in the plating bath, and the like, and the Al alloy raw material are included. Examples of the inevitable impurities include Cr, Cu, Mo, Ni, Ti, and Zr. Although the total content of Fe and inevitable impurities is not particularly limited, it is preferably 1% or less from the viewpoint of maintaining the corrosion resistance and uniform solubility of the plating layer.
The plating layer is a molten Al-based plating, and Zn is not contained unless it is an inevitable impurity.
本発明の溶融Ａｌ系めっき鋼板に用いられる下地鋼板の種類については、特に限定はされない。例えば、酸洗脱スケールした熱延鋼板若しくは鋼帯、又は、それらを冷間圧延して得られた冷延鋼板若しくは鋼帯を用いることができる。 There are no particular limitations on the type of base steel sheet used in the hot-dip Al-based plated steel sheet of the present invention. For example, a hot-rolled steel plate or steel strip that has been pickled and descaled, or a cold-rolled steel plate or steel strip obtained by cold rolling them can be used.
なお、めっき層の成分組成は、例えば、めっき層を塩酸等の水溶液に浸漬して溶解させ、その溶液をＩＣＰ発光分光分析や原子吸光分析を行うことで確認することができる。この方法はあくまでも一例であり、めっき層の成分組成を正確に定量できる方法であればどのような方法でも良く、特に限定するものではない。 The component composition of the plating layer can be confirmed by, for example, immersing and dissolving the plating layer in an aqueous solution such as hydrochloric acid, and performing the ICP emission spectroscopic analysis or atomic absorption analysis on the solution. This method is merely an example, and any method may be used as long as the component composition of the plating layer can be accurately quantified, and the method is not particularly limited.
なお、本発明の溶融Ａｌ系めっき鋼板のめっき層の付着量は片面あたり３５〜１５０ｇ／ｍ2であることが好ましい。３５ｇ／ｍ2以上であれば優れた耐食性が得られ、１５０ｇ／ｍ2以下であれば優れた加工性が得られるからである。また、より優れた耐食性及び加工性を得る点からは、前記付着量を、４０〜１１０ｇ／ｍ2とすることが好ましく、４０〜８０ｇ／ｍ2とすることがより好ましい。 In addition, it is preferable that the adhesion amount of the plating layer of the hot-dip Al system plated steel plate of this invention is 35-150 g / m < 2 > per single side | surface. This is because excellent corrosion resistance can be obtained at 35 g / m 2 or more, and excellent workability can be obtained at 150 g / m 2 or less. Further, more excellent from the viewpoint of obtaining a corrosion resistance and workability, the adhesion amount is preferably to 40~110g / m 2, and more preferably to 40 and 80 g / m 2.
次に、本発明の溶融Ａｌ系めっき鋼板の製造方法について説明する。
本発明の溶融Ａｌ系めっき鋼板は、連続式溶融めっき設備で製造され、めっき浴の組成管理以外は、全て常用の方法で行うことができる。
Next, the manufacturing method of the hot dip Al system plated steel plate of this invention is demonstrated.
The hot-dip Al-based plated steel sheet of the present invention is manufactured with a continuous hot-dip plating facility, and all can be performed by a conventional method except for composition management of the plating bath.
めっき浴中に、Ａｌに加え、Ｓｎを０．０１〜１０％含有させる。このような組成のめっき浴を用いることにより、上述しためっき層の構成を具える溶融Ａｌ系めっき鋼板を製造できる。その際、前述の通り、界面合金層の成長を抑制するために、めっき浴中にＳｉを０．１〜１０％含有させることが好ましい。また、腐食生成物の安定化効果を確保する点からは、Ｍｇ及び／又はＣａを、合計で０．０１〜１０質量％含有させることが好ましい。さらに、製造される溶融Ａｌ系めっき鋼板が安定的に優れた耐食性を得るために、Ａｌ含有量を９０％超えとすることが好ましい。 In addition to Al, 0.01 to 10% of Sn is contained in the plating bath. By using a plating bath having such a composition, a hot-dip Al-based plated steel sheet having the above-described configuration of the plating layer can be produced. At that time, as described above, in order to suppress the growth of the interface alloy layer, it is preferable to contain 0.1 to 10% of Si in the plating bath. Moreover, from the point which ensures the stabilization effect of a corrosion product, it is preferable to contain Mg and / or Ca 0.01 to 10 mass% in total. Furthermore, it is preferable that the Al content is more than 90% so that the manufactured molten Al-based plated steel sheet stably obtains excellent corrosion resistance.
上記のように、めっき浴の組成管理を行うことで、塗装後耐食性に優れる溶融Ａｌ系めっき鋼板を、連続的な溶融めっき設備で効率的に製造することができる。 As described above, by performing composition management of the plating bath, a hot-dip Al-based plated steel sheet having excellent post-coating corrosion resistance can be efficiently produced with continuous hot-dip plating equipment.
次に、本発明を実施例に基づき具体的に説明する。
（サンプル１〜２７）
サンプルとなる全ての溶融Ａｌ系めっき鋼板について、常法で製造した板厚０．８ｍｍの冷延鋼板を下地鋼板として用い、連続式溶融めっき設備によって、めっき浴の浴温を６００℃、めっき付着量を片面あたり５０ｇ／ｍ2、すなわち両面で１００ｇ／ｍ2の条件で製造した。
Next, the present invention will be specifically described based on examples.
(Samples 1-27)
For all the hot-dip Al-based plated steel sheets used as samples, cold-rolled steel sheets with a thickness of 0.8 mm manufactured in a conventional manner are used as the base steel sheet, and the bath temperature of the plating bath is 600 ° C with a continuous hot-dip plating facility. The amount was 50 g / m 2 per side, ie, 100 g / m 2 on both sides.
（１）めっき層の組成
サンプルとなる溶融Ａｌ系めっき鋼板を、それぞれ１００ｍｍΦに打ち抜き、３５％の塩酸水溶液に浸漬してめっき層を溶解させた後、溶解液の組成をＩＣＰ発光分光分析で定量化することで確認した。各サンプルの組成を表１に示す。
(1) Composition of plated layer Each sample of molten Al-based plated steel sheet was punched to 100 mmΦ, immersed in 35% hydrochloric acid aqueous solution to dissolve the plated layer, and then the composition of the dissolved solution was quantified by ICP emission spectroscopic analysis. It was confirmed by converting. The composition of each sample is shown in Table 1.
（２）塗装後耐食性の評価
サンプルとなる溶融Ａｌ系めっき鋼板をそれぞれ９０ｍｍ×７０ｍｍのサイズに剪断後、自動車外板用塗装処理と同様に、化成処理としてリン酸亜鉛処理を行った後、電着塗装、中塗り、及び上塗り塗装を施した。ここで、リン酸亜鉛処理、電着塗装、中塗り塗装及び上塗り塗装は以下に示す条件で行った。
○リン酸亜鉛処理：日本パーカライジング社製の脱脂剤：ＦＣ−Ｅ２００１、表面調整剤：ＰＬ−Ｘ、及び化成処理剤：ＰＢ−ＡＸ３５Ｍ（温度：３５℃）を用いて、化成処理液のフリーフッ素濃度を２００質量ｐｐｍ、化成処理液の浸漬時間を１２０秒の条件で化成処理を施した。
○電着塗装：関西ペイント社製の電着塗料：ＧＴ−１００を用いて、膜厚が１５μｍとなるように電着塗装を施した。
○中塗り塗装：関西ペイント社製の中塗り塗料：ＴＰ−６５−Ｐを用いて、膜厚が３０μｍとなるようにスプレー塗装を施した。
○上塗り塗装：関西ペイント社製の中塗り塗料：Ｎｅｏ６０００を用いて、膜厚が３０μｍとなるようにスプレー塗装を施した。
その後、図１に示すとおり、評価面の端部５ｍｍ、及び非評価面（背面）をテープでシール処理を行った後、評価面の中央にカッターナイフでめっき鋼板の地鉄に到達する深さまで、長さ６０ｍｍ、中心角９０°のクロスカット傷を加えたものを塗装後耐食性の評価用サンプルとした。
上記評価用サンプルを用いて図２に示すサイクルで腐食促進試験を実施した。腐食促進試験を湿潤からスタートし、６０サイクル後まで行った後、傷部からの塗膜膨れが最大である部分の塗膜膨れ幅（最大塗膜膨れ幅：傷部を中央にした片側の最大塗膜膨れ幅）を測定し、塗装後耐食性を下記の基準で評価した。評価結果を表１に示す。
○：最大塗膜膨れ幅≦１．５ｍｍ
△：１．５ｍｍ＜最大塗膜膨れ幅≦２．０ｍｍ
×：最大塗膜膨れ幅＞２．０ｍｍ
(2) Evaluation of corrosion resistance after painting After the molten Al-based plated steel sheet as a sample was sheared to a size of 90 mm x 70 mm, after the zinc phosphate treatment was performed as a chemical conversion treatment in the same manner as the coating treatment for automobile outer plates, A finish coating, intermediate coating, and top coating were applied. Here, the zinc phosphate treatment, electrodeposition coating, intermediate coating, and top coating were performed under the following conditions.
○ Zinc phosphate treatment: Defluorinating agent manufactured by Nihon Parkerizing Co., Ltd .: FC-E2001, surface conditioning agent: PL-X, and chemical conversion treatment agent: PB-AX35M (temperature: 35 ° C.) Chemical conversion treatment was performed under the conditions of a concentration of 200 mass ppm and an immersion time of the chemical conversion solution of 120 seconds.
Electrodeposition coating: Electrodeposition coating manufactured by Kansai Paint Co., Ltd .: Using GT-100, electrodeposition coating was applied so that the film thickness was 15 μm.
○ Intermediate coating: Using Kansai Paint Co., Ltd., intermediate coating: TP-65-P, spray coating was applied to a film thickness of 30 μm.
○ Top coating: Spray coating was performed using an intermediate coating paint: Neo6000 manufactured by Kansai Paint Co., Ltd. so that the film thickness was 30 μm.
Thereafter, as shown in FIG. 1, after the end of the
A corrosion acceleration test was performed in the cycle shown in FIG. 2 using the sample for evaluation. After starting the corrosion acceleration test from wet and after 60 cycles, the film bulge width of the part where the film bulge from the damaged part is maximum (maximum film bulge width: maximum on one side with the wound part in the center) (Coating swelling width) was measured, and the corrosion resistance after coating was evaluated according to the following criteria. The evaluation results are shown in Table 1.
○: Maximum coating film swelling width ≦ 1.5 mm
Δ: 1.5 mm <maximum paint film bulging width ≦ 2.0 mm
×: Maximum coating film swelling width> 2.0 mm
（３）めっきの外観品位
サンプルとなる溶融Ａｌ系めっき鋼板について、めっき処理を施した後１時間以内に、雰囲気：大気、温度：２０℃、相対湿度：５０％に調節した恒温恒湿槽内に入れた。以後、９０日間放置した後、サンプルを取り出しめっき表面の目視観察を行い、下記の基準で外観品位を評価した。評価結果を表１に示す。
○：黒変が認められない
△：黒変は認められるが、塗装を施さない用途で特に問題にならない
×：黒変が塗装を施さない用途で問題になる
(3) Appearance quality of the plating In a constant temperature and humidity chamber adjusted to atmosphere: air, temperature: 20 ° C., relative humidity: 50% within 1 hour after the plating treatment of the sampled hot Al plated steel sheet Put it in. Thereafter, after leaving for 90 days, the sample was taken out and visually observed on the plating surface, and the appearance quality was evaluated according to the following criteria. The evaluation results are shown in Table 1.
○: Blackening is not recognized Δ: Blacking is recognized, but there is no particular problem in applications where no coating is applied. ×: Blackening is a problem in applications where coating is not applied.
表１より、本発明例のサンプルでは、比較例のサンプルとは異なり、最大塗膜膨れ幅が２．０ｍｍ以下であったことから、塗装後耐食性に優れた溶融Ａｌ系めっき鋼板が得られたことがわかる。
また、本発明例のサンプルの中において、めっき層中のＳｎ含有量をそれぞれ適切な範囲に制御することで、塗装後耐食性に加えて、優れた外観品位が得られることがわかる。
さらに、本発明例のサンプルの中において、めっき層中のＭｇ含有量及び／又はＣａ含有量を適切な範囲に制御することで、より優れた塗装後耐食性が得られることがわかる。
From Table 1, the sample of the present invention sample, unlike the sample of the comparative example, had a maximum coating film swell width of 2.0 mm or less, and thus a molten Al-based plated steel sheet having excellent corrosion resistance after coating was obtained. I understand that.
Moreover, in the sample of this invention example, it turns out that the outstanding external appearance quality is obtained in addition to the corrosion resistance after a coating by controlling Sn content in a plating layer to an appropriate range, respectively.
Furthermore, it turns out that the more outstanding post-coating corrosion resistance is obtained by controlling Mg content and / or Ca content in a plating layer in a suitable range in the sample of this invention example.
本発明の溶融Ａｌ系めっき鋼板は、塗装後耐食性に優れ、自動車、家電、建材の分野等、広範な分野で適用できる。特に自動車分野において、高強度鋼板に適用すると、自動車の軽量化と高耐食性を達成する表面処理鋼板として使用できる。 The hot-dip Al-based plated steel sheet of the present invention has excellent post-painting corrosion resistance and can be applied in a wide range of fields such as automobiles, home appliances, and building materials. In particular, in the automobile field, when applied to a high-strength steel sheet, it can be used as a surface-treated steel sheet that achieves weight reduction and high corrosion resistance of the automobile.
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| JP2020122203A (en) * | 2019-01-31 | 2020-08-13 | Ｊｆｅスチール株式会社 | Al-BASED PLATED SHEET STEEL AND MANUFACTURING METHOD THEREOF |
| US20210292914A1 (en) * | 2020-03-17 | 2021-09-23 | Airbus Operations Gmbh | Anticorrosion coating and article coated with an anticorrosion coating, especially for use in an aircraft |
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| JPH0611918B2 (en) * | 1989-06-13 | 1994-02-16 | 日本鋼管株式会社 | Surface-treated steel plate for cans |
| JP2001081539A (en) * | 1999-09-10 | 2001-03-27 | Nippon Steel Corp | Hot dip aluminum plated steel sheet excellent in high temperature corrosion resistance and its manufacture |
| JP2001192799A (en) * | 1999-10-29 | 2001-07-17 | Nippon Steel Corp | High strength hot-dip metal coated steel sheet excellent in workability, and its manufacturing method |
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|---|---|---|---|---|
| JPH0611918B2 (en) * | 1989-06-13 | 1994-02-16 | 日本鋼管株式会社 | Surface-treated steel plate for cans |
| JP2001081539A (en) * | 1999-09-10 | 2001-03-27 | Nippon Steel Corp | Hot dip aluminum plated steel sheet excellent in high temperature corrosion resistance and its manufacture |
| JP2001192799A (en) * | 1999-10-29 | 2001-07-17 | Nippon Steel Corp | High strength hot-dip metal coated steel sheet excellent in workability, and its manufacturing method |
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| JP2020122203A (en) * | 2019-01-31 | 2020-08-13 | Ｊｆｅスチール株式会社 | Al-BASED PLATED SHEET STEEL AND MANUFACTURING METHOD THEREOF |
| US20210292914A1 (en) * | 2020-03-17 | 2021-09-23 | Airbus Operations Gmbh | Anticorrosion coating and article coated with an anticorrosion coating, especially for use in an aircraft |
| US11959180B2 (en) * | 2020-03-17 | 2024-04-16 | Airbus Operations Gmbh | Anticorrosion coating and article coated with an anticorrosion coating, especially for use in an aircraft |
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