JP3735360B2 - Manufacturing method of hot-dip Zn-Mg-Al plated steel sheet with excellent appearance - Google Patents
Manufacturing method of hot-dip Zn-Mg-Al plated steel sheet with excellent appearance Download PDFInfo
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Description
本発明は、めっき外観に優れた溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の製造方法に関するものである。 The present invention relates to a method for producing a hot-dip Zn—Mg—Al-plated steel sheet having an excellent plating appearance.
耐食性に優れる溶融Ｚｎ−Ｍｇ−Ａｌめっき鋼板については従来より幾つかの提案がなされており、例えば本発明者らも特許文献１で、Ｚｎ−Ｍｇ−Ａｌめっき鋼板の製造方法を提案している。
その方法は、還元処理した鋼板、あるいはプレＮｉめつきした鋼板を４６０〜５５０℃の範囲で、Ａｌ：０．１〜４０％、Ｍｇ：０．１〜１０％含有するＺｎめっき浴に浸漬して溶融めっきし、浴より引き上げた溶融めっき鋼板を、慣用のガスワイピングによりめつき付着量調整後、冷却してめつき層を凝固させるものである。尚、めっき層中にＭｇ金属間化合物相を分散させるために、めっき層がまだ溶融状態のうちに冷却速度を５゜Ｃ／ｓｅｃ以上程度に制御することなどが望ましいと述べている。
The method is to immerse a reduction-treated steel plate or a pre-Ni-plated steel plate in a Zn plating bath containing Al: 0.1 to 40% and Mg: 0.1 to 10% within a range of 460 to 550 ° C. The hot dip galvanized steel sheet that has been hot dip-plated and pulled up from the bath is cooled to adjust the adhesion amount by conventional gas wiping, and then cooled to solidify the adhesion layer. It is stated that it is desirable to control the cooling rate to about 5 ° C./sec or more while the plating layer is still in a molten state in order to disperse the Mg intermetallic compound phase in the plating layer.
このような方法で得られた溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板は、建材、土木分野のガードレール、防音壁、家電分野の部品等を中心に寿命延長の観点から高耐食性めっき鋼板として多く使用されており、優れためっき鋼板であるが、めっき層の凝固組織がＺｎ−Ｍｇ合金相、Ａｌの含有量に応じてＺｎ初晶、あるいはＡｌ初晶よりなる複雑な構造をしているため、冷却速度をコントロールしないと外観上、斑点〔Ｚｎ−Ｍｇ−Ａｌ３元合金相起因〕あるいは表面の梨地状の微小凹凸（Ａｌ初晶起因）、白いざらつき、微小羽根模様等が生じることがあり、その改善が望まれていた。 The hot-dip Zn-Mg-Al-based plated steel sheet obtained by such a method is often used as a highly corrosion-resistant plated steel sheet from the viewpoint of extending the life centering on building materials, guardrails in the civil engineering field, soundproof walls, parts in the home appliance field, etc. It is an excellent plated steel sheet, but the solidification structure of the plating layer has a complex structure consisting of Zn primary crystals or Al primary crystals depending on the Zn-Mg alloy phase and Al content. If the speed is not controlled, the appearance may cause speckles (due to the Zn-Mg-Al ternary alloy phase) or surface textured fine irregularities (due to Al primary crystals), white roughness, fine feather patterns, etc. Was desired.
本発明者らは、その後種々検討したところ、溶融Ｚｎ−Ｍｇ−Ａｌめっき鋼板の製造プロセスにおいて、ワイピング後、未凝固状態のめっき鋼鈑表面に固体表面を接触させることでめっき層中に凝固核を生成させることにより、その後どのような冷却速度で冷却しても、斑点〔Ｚｎ−Ｍｇ−Ａｌ３元合金相起因〕あるいは表面の梨地状の微小凹凸（Ａｌ初晶起因）、微小羽根模様等が解消し優れた均一外観となることを見出し、下記の本発明を完成したものである。 The inventors of the present invention subsequently studied variously, and in the manufacturing process of the molten Zn-Mg-Al plated steel sheet, after wiping, the solid surface was brought into contact with the surface of the unsolidified plated steel sheet by bringing the solid surface into contact with the solidified nucleus. After forming, no matter what the cooling rate is, spots [because of Zn-Mg-Al ternary alloy phase] or surface-like fine irregularities (because of Al primary crystal), fine feather patterns, etc. The present invention described below has been completed by finding that it has been solved and has an excellent uniform appearance.
即ち本発明は、鋼板をＡｌ：０．１−６０％、Ｍｇ：０．１−１０％含有するＺｎめつき浴に浸漬し、浴より引き上げた溶融めっき鋼板をガスワイピングによってめつき付着量調整後、冷却してめつき層を凝固させる溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の製造方法において、めつき付着量調整後、冷却前に未凝固状態のめつき層表面に固体表面を接触させることにより、めっき層中に凝固核を生成させることを特徴とする外観に優れた溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の製造方法である。 That is, in the present invention, the steel sheet is immersed in a Zn plating bath containing Al: 0.1-60% and Mg: 0.1-10%, and the amount of adhesion is adjusted by gas wiping of a hot-dip plated steel plate pulled up from the bath. Then, in the method of manufacturing a molten Zn—Mg—Al-plated steel sheet that cools and solidifies the adhesion layer, after adjusting the adhesion amount of adhesion, the solid surface is brought into contact with the surface of the unsolidified adhesion layer before cooling. Is a method for producing a hot-dip Zn—Mg—Al-plated steel sheet having an excellent appearance, characterized in that solidification nuclei are generated in the plating layer.
上記未凝固状態のめつき層表面に接触させる固体表面が凹凸を有しており、その平均深さで０．０１〜５００μｍ、凹凸間の平均距離が３０００μｍとなるようにすることができる。 The solid surface brought into contact with the surface of the unsolidified adhesive layer has irregularities, and the average depth can be 0.01 to 500 μm, and the average distance between the irregularities can be 3000 μm.
また、上記Ｚｎめつき浴中にＳｉ，Ｓｎ，Ｃｒ，Ｔｉ，Ｂ，Ｎｉ，Ｆｅ，Ｃｏ，Ｓｂ，Ｐｂ，Ｃｕの元素を単独あるいは複合で１０％以下含有させることができる。 Further, in the Zn plating bath, elements of Si, Sn, Cr, Ti, B, Ni, Fe, Co, Sb, Pb and Cu can be contained alone or in combination of 10% or less.
さらに本発明は、前記した未凝固状態のめつき層中に凝固核を生成させた後、冷却速度５℃／秒以上の空冷あるいは気水冷却をすることができる。 Furthermore, in the present invention, after generating solidified nuclei in the above-mentioned unsolidified adhesive layer, air cooling or air-water cooling at a cooling rate of 5 ° C./second or more can be performed.
さらに本発明は、上記した方法において、鋼板表面にＮｉを０．２〜１０ｇ／ｍ2 プレめつき後、加熱（４６０〜５５０℃）し、この鋼板をめっき浴に浸漬する方法も採用できる。 Furthermore, the present invention can employ a method in which Ni is 0.2 to 10 g / m 2 pre-plated on the surface of the steel sheet and then heated (460 to 550 ° C.) and the steel sheet is immersed in a plating bath.
さらには還元処理した（４６０〜５５０℃の）鋼板をめっき浴に浸漬することもできる。 Furthermore, a reduction-treated steel plate (from 460 to 550 ° C.) can be immersed in the plating bath.
このように本発明は、上記した各処理を適宜採用することにより、外観に優れた溶融Ｚｎ−Ｍｇ−Ａｌめっき鋼板を製造することができる。 Thus, this invention can manufacture the hot-dip Zn-Mg-Al plating steel plate excellent in the external appearance by employ | adopting each above-mentioned process suitably.
本発明のめっき製造方法は、Ｚｎ−Ｍｇ−Ａｌ系溶融めっきにおいて、後の冷却方法を選ばず外観が良好になる点で非常に有用である。 The plating production method of the present invention is very useful in terms of improving the appearance of any Zn-Mg-Al-based hot dipping, regardless of the subsequent cooling method.
以下に本発明の実施の形態を詳細に説明する。
本発明は、溶融Ｚｎ−Ｍｇ−Ａｌめっき鋼板の製造プロセスにおいて、ワイピング後、未凝固状態のめっき鋼板表面に固体表面を接触させるにより、めっき層中に凝固核を生成させ、これにより溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の外観が非常に良好となるところに最大の技術上のポイントがある。
Hereinafter, embodiments of the present invention will be described in detail.
In the manufacturing process of the molten Zn-Mg-Al plated steel sheet, the present invention generates solidified nuclei in the plated layer by bringing a solid surface into contact with the surface of the unsolidified plated steel sheet after wiping. The biggest technical point is that the appearance of the Mg—Al-based plated steel sheet is very good.
以下に本発明における各条件の限定理由について述べる。
まず、Ａｌ：０．１〜６０％、Ｍｇ：０．１〜１０％、残りＺｎ及び不可避成分よりなる溶融Ｚｎ−Ｍｇ−Ａｌめっき鋼板の製造プロセスとしたのは、本組成範囲において本発明のポイントとなるプロセスである未凝固状態のめっき鋼板表面に固体表面を接触させることにより、めっき層中に凝固核を生成させめっき外観が良好となる効果が最も出やすいためである。
The reasons for limiting each condition in the present invention will be described below.
First, the manufacturing process of the hot-dip Zn—Mg—Al-plated steel sheet composed of Al: 0.1 to 60%, Mg: 0.1 to 10%, the remaining Zn and inevitable components was used in the present composition range. This is because by bringing the solid surface into contact with the surface of the unsolidified plated steel sheet, which is a key process, the effect of generating solidified nuclei in the plating layer and improving the plating appearance is most likely to occur.
また、ワイピング後、未凝固状態のめっき鋼板表面に固体表面を接触させこととしたのは、未凝固状態の時でないとめっき層中に凝固核が生成しないためである。
さらには、未凝固状態のめっき鋼板表面に接触させる固体表面が凹凸を有していると、めっき表面外観が良好となったためである。
In addition, the reason why the solid surface is brought into contact with the surface of the unsolidified plated steel sheet after wiping is that solidification nuclei are not generated in the plating layer unless the solid surface is in an unsolidified state.
Furthermore, when the solid surface brought into contact with the surface of the unsolidified plated steel sheet has irregularities, the appearance of the plated surface is improved.
そのメカニズムは未だ明確ではないが、固体表面の凹凸により、Ｚｎ−Ｍｇ−Ａｌ系めっき層中に発生する初期凝固核の数、核の距離などが影響を受け、Ａｌ初晶あるいはＺｎ初晶及び３元Ｚｎ−Ｍｇ−Ａｌ合金相、さらにはＺｎ−Ｍｇ−ＡｌめっきにＳｉあるいはＳｎを含有する場合には、Ｍｇ2 Ｓｉ、Ｍｇ2 Ｓｎ金属間化合物などの生成状態が変化し、上述の斑点、表面の梨地状の微小凹凸（Ａｌ初晶起因）、白いざらつき、微小羽根模様等が解消し、外観向上につながっているものと思われる。 Although the mechanism is not yet clear, the number of initial solidification nuclei generated in the Zn—Mg—Al-based plating layer, the distance of the nuclei, etc. are affected by the unevenness of the solid surface. When Si or Sn is contained in the ternary Zn—Mg—Al alloy phase and further Zn—Mg—Al plating, the production state of Mg 2 Si, Mg 2 Sn intermetallic compound, etc. changes, and the above-mentioned spots It seems that the textured surface irregularities (because of Al primary crystal), white roughness, fine feather pattern, etc. have been eliminated, leading to improved appearance.
接触させる装置については特に限定しないが、水冷銅ロール、ベルトキャスター、ウオーキングバーなどが使用でき、接触させる固体の種類についても銅そのもの、あるいはその表面に金属めっき、セラミックコーティングを施したものなどいろいろ使用できる。 There are no particular restrictions on the device to be contacted, but water-cooled copper rolls, belt casters, walking bars, etc. can be used, and various types of solids to be contacted, such as copper itself or metal plating or ceramic coating on its surface, can be used. it can.
ワイピング後、未凝固状態のめっき鋼板表面に固体表面を接触させることによりめっき層中に凝固核を生成させた後に、冷却速度５℃／ｓ以上の空冷あるいは気水冷却することとしたのは、本未凝固状態のめっき鋼板表面に固体表面を接触させる工程により、その後の冷却が空冷であっても気水冷却であっても平滑な美しい表面外観が確保でき、特に冷却速度を５℃／ｓ以上でその効果が顕著なためである。また固体表面接触後、気水冷却を行うと冷却速度が早いために、平滑な外観に加えてめっき結晶粒の微細化及びめっき層中のＭｇ2 Ｓｉ等の析出物の均一分散化も可能なためである。 After wiping, solidified nuclei were generated in the plated layer by bringing the solid surface into contact with the surface of the unsolidified plated steel sheet, and then air cooling or air-water cooling at a cooling rate of 5 ° C./s or more was performed. The step of bringing the solid surface into contact with the surface of the unsolidified plated steel sheet can ensure a smooth and beautiful surface appearance regardless of whether the subsequent cooling is air cooling or air-water cooling. This is because the effect is remarkable. In addition, since the cooling rate is fast when air-water cooling is performed after contact with the solid surface, it is possible to refine the plating crystal grains and uniformly disperse precipitates such as Mg 2 Si in the plating layer in addition to a smooth appearance. Because.
これらのメカニズムも未だ明確ではないが、未凝固状態のめっき鋼板表面に固体表面を接触させるによりめっき層中に凝固核を生成させた場合、この凝固核が後に空冷あるいは気水凝固してもそのまま保持され、表面の外観を保つ効果があるものと思われる。 These mechanisms are still unclear, but when solidified nuclei are generated in the plating layer by bringing the solid surface into contact with the surface of the unsolidified plated steel sheet, the solidified nuclei will remain as they are even after solidification by air cooling or air-water solidification. It seems that it is retained and has the effect of maintaining the appearance of the surface.
さらに、めっき浴の組成としてＡｌ：０．１〜４０％、Ｍｇ：０．１〜１０％含有するＺｎ−Ａｌ―Ｍｇ合金浴、もくは本溶融Ｚｎ−Ｍｇ−Ａｌめっき浴中にＳｉ，Ｓｎ，Ｃｒ，Ｔｉ，Ｂ，Ｎｉ，Ｆｅ，Ｃｏ，Ｓｂ，Ｐｂ，Ｃｕの元素を単独あるいは複合で１０以下含有するめっき浴としたのは、本範囲においてめっき層の耐食性が極めて良好となるためである。 Further, the composition of the plating bath is Al: 0.1 to 40%, Mg: 0.1 to 10% of Zn-Al-Mg alloy bath, or in the present molten Zn-Mg-Al plating bath, Si, The reason why the plating bath containing the elements of Sn, Cr, Ti, B, Ni, Fe, Co, Sb, Pb, and Cu alone or in combination is 10 or less is that the corrosion resistance of the plating layer is extremely good in this range. It is.
次にＮｉプレめっき量を０．２〜１０ｇ／ｍ2 としたのは、この範囲でめっき性が良好となるためである。プレＮｉ量が０．２ｇ／ｍ2 未満では、溶融めっき時に微小不めっきが生じ、１０ｇ／ｍ2 を超えるとめっき密着性がやや劣化するからである。
さらに、還元処理した４６０〜５５０℃の鋼板を浴浸することとしたのは、プレＮｉめっきなしの場合のめっきにも本方法が効果があったためである。
Next, the reason why the Ni pre-plating amount is set to 0.2 to 10 g / m 2 is that the plating property is good in this range. This is because if the amount of pre-Ni is less than 0.2 g / m 2 , minute non-plating occurs at the time of hot dipping, and if it exceeds 10 g / m 2 , the plating adhesion is slightly deteriorated.
Furthermore, the reason why the reduced-treated 460 to 550 ° C. steel sheet is bath-immersed is that the present method was effective in plating without pre-Ni plating.
溶融めっきの付着量については特に制約は設けないが、耐食性の観点から１０ｇ／ｍ2 以上、加工性の観点からすると３５０ｇ／ｍ2 以下であることが望ましい。
なお、本発明の下地鋼板としては、熱延鋼板、冷延鋼板共に使用でき、鋼種もＡｌキルド鋼、Ｔｉ，Ｎｂ等を添加した極低炭素鋼板、およびこれらにＰ，Ｓｉ，Ｍｎ等の強化元素を添加した高強度鋼、ステンレス鋼板など種々のものが適用できる。
Although there is no particular restriction on the adhesion amount of the hot dipping, it is preferably 10 g / m 2 or more from the viewpoint of corrosion resistance and 350 g / m 2 or less from the viewpoint of workability.
In addition, as a base steel plate of the present invention, both hot-rolled steel plates and cold-rolled steel plates can be used, and steel grades are ultra-low carbon steel plates to which Al killed steel, Ti, Nb, etc. are added, and reinforced with P, Si, Mn, etc. Various materials such as high-strength steel added with elements and stainless steel plate can be applied.
以下、実施例によって本発明をさらに詳細に説明する。
（実施例１）
表面粗度（３，１０，１００μｍ）の変化した水冷Ｃｕ板で溶融状態のＺｎ−３％Ｍｇ−１１％Ａｌ−０．２％Ｓｉ（一部Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ、Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ−０．２％Ｓｉ、一部Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ−５％Ｓｎ）めっき表面をワイピング後に４００℃で１ｓｅｃタッチを行った後、自然放冷、空冷（ガスジェット：ＡＪＣ）及び気水冷却、水冷で冷却した場合の外観の変化、ミクロ構造を表１に示す。
比較には、空冷のみ、気水冷却のみの場合を示した。
溶融めっき条件は、熱延酸洗鋼板１．６ｍｍにプレＮｉめっきを１ｇ／ｍ2 施した後、板温度４５０℃まで加熱し、４５０℃のめっき浴中で溶融めっきした。めっき付着量は、片面１３５ｇ／ｍ2 とした。
Hereinafter, the present invention will be described in more detail with reference to examples.
Example 1
Zn-3% Mg-11% Al-0.2% Si (partially Zn-0.5% Mg-0.2%) in a molten state with a water-cooled Cu plate having a changed surface roughness (3, 10, 100 μm) Al, Zn-0.5% Mg-0.2% Al-0.2% Si, partially Zn-0.5% Mg-0.2% Al-5% Sn) After wiping the plating surface at 400 ° C Table 1 shows changes in appearance and microstructure when cooled by natural cooling, air cooling (gas jet: AJC), air-water cooling, and water cooling after touching for 1 sec.
For comparison, only air cooling and air / water cooling were shown.
The hot-dip pickled steel sheet 1.6 mm was subjected to pre-Ni plating 1 g / m 2 and then heated to a plate temperature of 450 ° C. and hot-dip plated in a 450 ° C. plating bath. The plating adhesion amount was set to 135 g / m 2 on one side.
表１から明らかなように、本発明の溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の製造方法（Ｎｏ．１〜８，１１〜１３）は、比較の方法（Ｎｏ．９，１０）に比べて、めっき外観が良好である。 As apparent from Table 1, the production method (Nos. 1 to 8, 11 to 13) of the hot-dip Zn—Mg—Al-plated steel sheet of the present invention is compared to the comparative method (Nos. 9 and 10). The plating appearance is good.
（実施例２）
鏡面仕上げした水冷Ｃｕロール（表面凹凸の平均深さ０．０５μｍ、表面凹凸の平均距離２５００μｍ）およびその上にＣｒめっきを２０μｍ施した水冷Ｃｕロール（表面凹凸の平均深さ０．１μｍ、表面凹凸の平均距離２０００μｍ）あるいはＮｉ−Ｗめっきを５μｍ施した水冷Ｃｕロール（表面凹凸の平均深さ０．１μｍ、表面凹凸の平均距離１８００μｍ）で溶融状態のＺｎ−３％Ｍｇ−１１％Ａｌ−０．２％Ｓｉ（一部Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ、Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ−０．２％Ｓｉ、一部Ｚｎ−０．５％Ｍｇ−０．２％Ａｌ−５％Ｓｎ）めっき表面をワイピング後に４００℃で１ｓｅｃタッチを行った後、自然放冷、空冷（ガスジェット：ＡＪＣ）及び気水冷却、水冷で冷却した場合の外観の変化、ミクロ構造を表２に示す。
比較には、空冷のみ、気水冷却のみの場合を示した。
溶融めっき条件は、熱延酸洗鋼板１．６ｍｍにプレＮｉめっきを１ｇ／ｍ2 施した後、板温度４５０℃まで加熱し、４３０℃のめっき浴中で溶融めっきした。めっき付着量は、片面９０ｇ／ｍ2 とした。
(Example 2)
Mirror-finished water-cooled Cu roll (average depth of surface irregularities 0.05 μm, average distance of surface irregularities 2500 μm) and water-cooled Cu roll with 20 μm of Cr plating thereon (average depth of surface irregularities 0.1 μm, surface irregularities) Zn-3% Mg-11% Al-0 in a molten state with a water-cooled Cu roll (average depth of surface irregularities 0.1 μm, average distance of surface irregularities 1800 μm) subjected to Ni-W plating 5 μm .2% Si (partially Zn-0.5% Mg-0.2% Al, Zn-0.5% Mg-0.2% Al-0.2% Si, part Zn-0.5% Mg -0.2% Al-5% Sn) After wiping the plating surface for 1 second at 400 ° C., the appearance of natural cooling, air cooling (gas jet: AJC), air / water cooling, and water cooling Change, microstructure It shows in Table 2.
For comparison, only air cooling and air / water cooling were shown.
The hot-dip pickled steel sheet 1.6 mm was subjected to pre-Ni plating 1 g / m 2, then heated to a plate temperature of 450 ° C. and hot-dip plated in a 430 ° C. plating bath. The amount of plating was 90 g / m 2 on one side.
表２から明らかなように、本発明の溶融Ｚｎ−Ｍｇ−Ａｌ系めっき鋼板の製造方法（Ｎｏ．１〜９，１２−１４）は、比較の方法（Ｎｏ．１０，１１）に比べてめっき外観が良好である。 As apparent from Table 2, the production method (Nos. 1-9, 12-14) of the hot-dip Zn—Mg—Al-based plated steel sheet of the present invention is plated compared to the comparative method (Nos. 10, 11). Appearance is good.
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| JP4582707B2 (en) * | 2005-04-20 | 2010-11-17 | 新日本製鐵株式会社 | Hot-dip galvanizing method without generation of non-plating defects |
| JP4855290B2 (en) * | 2007-02-09 | 2012-01-18 | 新日本製鐵株式会社 | Hot-dip galvanized steel sheet and method for producing alloyed hot-dip galvanized steel sheet |
| WO2008136496A1 (en) * | 2007-04-27 | 2008-11-13 | Jfe Steel Corporation | Surface-treated, hot-dip zn-al alloy coated steel sheet |
| JP5317516B2 (en) * | 2007-04-27 | 2013-10-16 | Ｊｆｅスチール株式会社 | Surface-treated molten Zn-Al alloy-plated steel sheet |
| EP2250296B1 (en) * | 2008-03-13 | 2020-10-14 | Bluescope Steel Limited | Metal-coated steel strip and method of manufacturing thereof |
| JP5200851B2 (en) * | 2008-10-23 | 2013-06-05 | 新日鐵住金株式会社 | Zn-Al-Mg-based plated steel sheet and method for producing the same |
| KR101625556B1 (en) | 2009-03-13 | 2016-05-30 | 블루스코프 스틸 리미티드 | Corrosion protection with al/zn-based coatings |
| WO2011001662A1 (en) * | 2009-06-30 | 2011-01-06 | 新日本製鐵株式会社 | Zn-Al-Mg HOT-DIP COATED STEEL SHEET AND PROCESS FOR PRODUCTION THEREOF |
| US11236409B2 (en) * | 2017-03-17 | 2022-02-01 | Nippon Steel Corporation | Coated steel sheet |
| SG11201908425UA (en) * | 2017-03-17 | 2019-10-30 | Nippon Steel Corp | Coated steel sheet |
| JP7044998B2 (en) * | 2019-03-22 | 2022-03-31 | Ｊｆｅスチール株式会社 | Fused Zn-Al-based plated steel sheet and its manufacturing method |
| KR20220146586A (en) | 2020-03-30 | 2022-11-01 | 닛폰세이테츠 가부시키가이샤 | hot dip galvanized steel |
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