JP2004002933A - Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the aluminum plated steel sheet - Google Patents
Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the aluminum plated steel sheet Download PDFInfo
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Abstract
Description
【０００１】
【発明の属する技術分野】
本発明は、自動車用部品などに使用されるスポット溶接に代表される抵抗溶接を用いて接合されるアルミニウムめっき鋼板及び前記アルミニウムめっき鋼板を用いて加工された部品に関する。
【０００２】
【従来の技術】
薄鋼板を使用した自動車加工部品の多くは、車体組立工程にてスポット溶接に代表される抵抗溶接にて接合され車体を構成する。近年、車体防錆性能向上の要求から鋼板表面にめっきなどを施した表面処理鋼板の使用が拡大しているが、一的般に裸鋼板と比較して、表面処理鋼板は溶接性が低下する。低下する溶接性としては▲１▼適正溶接電流範囲が縮小すること、▲２▼電極寿命が低下すること、の２点が挙げられる。前者は、めっき金属の溶融に伴って通電面積が拡大し、充分なナゲットを得るために必要な電流・通電サイクルは裸鋼板よりも大きくなるが、チリ発生電流や溶着電流はナゲット形成電流の上昇ほど大きくならずに、結果として適正溶接電流範囲は縮小するというものである。後者は、電極として用いられる銅合金とめっき金属が溶接中に反応して合金層を形成して、電極表面が合金層に覆われて溶接品質が低下するというものである。
【０００３】
スポット溶接では電極先端径が拡大して電流密度が低下しナゲットが形成しなくなる現象が見られる。また、シーム溶接やプロジェクション溶接では合金層により電極表面の形状や抵抗が不均一となって通電が偏り、チリ発生やナゲット形状が悪化して接合強度が低下したり、穴明きが生じたりするなどの問題が生じる。この特性を改善する方法としては▲１▼皮膜によるバリア効果で合金化反応を抑制すること、▲２▼皮膜や溶接条件にて溶接時の抵抗を低減して、電極表面での合金化反応を抑制することが挙げられる。
【０００４】
めっき鋼板の中でもアルミニウムめっき鋼板は電極の銅合金との反応が顕著であり、溶接時の電極寿命を短かくせしめる種類の鋼板である。このアルミニウムめっき鋼板の電極寿命を向上させる技術としては、特開平１０−１８３３６８号公報、特開平１０−４６３５８号公報、特開平１０−３３０９５７号公報など、に開示された技術のようにアルミニウムめっき鋼板の表面に後処理皮膜を付与することで電極寿命を向上させるものがある。ただ、これらの技術でも得られる電極寿命は裸鋼板と比べると小さいものとなっていた。
【０００５】
【発明が解決しようとする課題】
本発明は、前記の溶接性の課題を解決して、抵抗溶接性に優れたアルミニウムめっき鋼板及びこれを用いた加工部品を提供するものである。
【０００６】
【課題を解決するための手段】
本発明者らは、上記課題を解決するために基礎的な検討を実施した。その結果、めっき層表面のＦｅ濃度とＳｉ濃度を適正化することにより抵抗溶接性に優れたアルミニウムめっき鋼板とこれを利用した加工部品が製造できることを見出した。すなわち、めっき金属と電極である銅合金との合金化は発熱によりめっき金属が溶融して反応性が増加することにより促進されるが、アルミニウムめっき層の表面のＦｅ濃度を上昇させ融点を上昇させることによりめっき表面の溶融が抑制されて、合金化が著しく抑制されることが考えられる。
【０００７】
また、アルミニウムめっき鋼板には通常、加工性を低下させるＦｅ−Ａｌ合金層の成長を抑制するためにＳｉが添加されているが、Ｓｉは電気抵抗を上昇させる元素であり、電極表面でのジュール発熱を促進して電極寿命に不利に作用することが考えられる。本発明者らは、めっき層の電気抵抗を低下させるためにＳｉ濃度を低下させることを知見した。
【０００８】
アルミニウムめっき鋼板を加熱してめっき層をＦｅ−Ａｌ合金とする技術は特開昭６０−２５１２６７号公報、特開２０００−３８６４０号公報に示されているが、両者ともＳｉにより電気抵抗を上昇させる技術については言及していない。また、特開平９−１１８９７０号公報には、アルミニウムめっき鋼板を耐熱性の観点から加熱処理する技術が開示されているが、Ｆｅのめっき層への拡散を抑制する技術思想であり表面でのＦｅ濃度についての開示はない。
【０００９】
本発明の要旨とするところは下記のとおりである。
（１）鋼板表面にＦｅ，Ａｌを主成分とする金属間化合物層を有し、金属間化合物層の表面から５μｍまでのＦｅの平均濃度が質量％で３０％以上で、かつＳｉの平均濃度が添加Ｓｉ量の６％以下であることを特徴とする抵抗溶接性に優れたアルミニウムめっき鋼板。
（２）（１）に記載のアルミニウムめっき鋼板を使用することを特徴とする抵抗溶接性に優れたアルミニウムめっき鋼板を用いた加工部品にある。
【００１０】
【発明の実施の形態】
以下に、本発明の制限範囲について詳細に説明する。
金属間化合物層の表面から５μｍまでのＦｅの平均濃度を３０％以上としたのは、これ以下のＦｅ濃度であると、めっき層表面の融点が充分上昇せず、抵抗溶接時にめっき層表面が溶融してめっき金属が電極材料である銅合金と合金化しやすくなり、電極寿命が低下するためである。そのＦｅの平均濃度については３０％以上で電極寿命は良好であるが、望ましくは４０％以上で充分な特性を示す。
【００１１】
金属間化合物層の表面から５μｍまでのＳｉの平均濃度を６％以下としたのは、６％超のＳｉ濃度ではめっき表面の電気抵抗が高くなって電極寿命が低下するためである。Ｆｅの平均濃度、Ｓｉの平均濃度を表面からの深さ５μｍまでの平均としたのは、これを超えての深さまでの平均濃度にすると、重要である最表面のＦｅ濃度、Ｓｉ濃度が反映されないためである。
【００１２】
上記の金属間化合物層を有する鋼板を加工した部品、また鋼板を高温に加熱した状態で成形するホットプレスなどにより上記の金属間化合物層を形成した部品は、抵抗溶接時にめっき層表面の溶融が抑制されてめっき金属と電極の合金化が抑制され、かつめっき層表面の電気抵抗が低いために発熱が抑制されて、優れた電極寿命を示す。鋼板の化学成分やミクロ組織は特に制限しないが、上記の金属間化合物層のめっき層を有していれば、優れた電極寿命を示す。
【００１３】
めっき層の構成としては、Ａｌを主成分としてＳｉを添加するものである。この他の添加元素としてＣｒ，Ｍｇ，Ｔｉ，Ｓｂ，Ｓｎ，Ｚｎ等が考えられるが、めっき層がＡｌを主体とする限り、適用可能である。しかし、Ｚｎは沸点が低く、大量に添加すると加熱時に表面に粉体状のＺｎを生成して、プレス時のカジリを惹起するため、６０％以上の添加は望ましくない。
本発明において、アルミニウムめっきの付着量、めっき前処理、後処理については特に限定するものではない。めっき付着量は通常の片面３０〜１００ｇ／ｍ２の範囲ではなんら問題ない。
【００１４】
めっき後処理として一次防錆、潤滑性を目的としてクロメート処理、樹脂被覆処理等ありうるが、有機樹脂は加熱すると消失してしまうため好ましくない。クロメート処理も近年の６価クロム規制を考慮すると、電解クロメート等の３価の処理皮膜が好ましい。
アルミニウムめっき鋼板の製造法についても何ら限定するものではない。通常の製鋼、熱延条件が適用可能である。アルミニウムめっきは通常溶融めっき法で施されるが、これに限定せず、非水溶媒からの電気めっき、蒸着処理等も使用可能である。めっき前処理としてＮｉプレめっき等のプレめっきもありうるが、これも適用可能である。
【００１５】
また、本発明のめっき層を実現するための手段も特に制限しないが、本発明の範囲を満足していれば優れた電極寿命を示す。考えられる方法としては、鋼板を高温で加熱して本発明を満足する金属間化合物層をめっき層とすることが考えられ、小型電気炉、連続焼鈍ライン、バッチ焼鈍ライン、高周波加熱など方法は問わない。表面の組成は熱処理条件を変更することで制御可能である。金属間化合物の表面組成を測定する方法としては、電子線マイクロアナライザー（ＥＰＭＡ）やエネルギー分散型Ｘ線分光計（ＥＤＸ）が精度の点で望ましい。
【００１６】
【実施例】
以下、本発明の実施例について説明する。
通常の熱延、冷延工程を経た、表１に示すような鋼成分の冷延鋼板（板厚１．２ｍｍ）を材料として、溶融アルミニウムめっきを行った。溶融アルミニウムめっきは無酸化炉−還元タイプのラインを使用し、めっき後ガスワイピング法でめっき付着量を両面８０ｇ／ｍ２と１２０ｇ／ｍ２に調節し、その後冷却し、ゼロスパングル処理を施した。この際のめっき浴組成を表２に示す。浴中のＦｅは浴中のめっき機器やストリップから供給される不可避のものである。めっき外観は不めっき等なく良好であった。めっき後、インラインにて表３に示す後処理を施し、インラインにて圧下率０．８％のスキンパス圧延を行った。
【００１７】
【表１】
【表２】
【表３】
以上の工程で得られたアルミニウムめっき鋼板を熱処理した。熱処理条件と方法を表４、５、６に示し、いくつかの試料については加熱後、ホットプレスを行った。ホットプレスを行った実験については、表４、５、６に凡例○で示す。また、いくつかの試料については冷却後に加工を行った。冷却後に加工を行った実験については、表４、５、６に凡例○で示す。また、表面５μｍまでの表面のＦｅ，Ｓｉ濃度を電子線アナライザーにて測定し、表４、５、６にあわせて示す。
【００２１】
得られた試料について、溶接試験を行い電極寿命を検討した。用いた抵抗溶接はスポット溶接であり、それらの条件を以下に示す。評価はナゲット径が４√ｔを切った時点までの連続打点数とした。ホットプレスを実施した実験についてはホットプレス部品、冷却後に加工した実験については加工部品、その他については鋼板について溶接評価を行った。
（溶接条件）
溶接電源：単相交流
溶接電流：チリ発生電流の９５％
加圧力：３００ｋｇｆ
溶接時間：１２サイクル（周波数：６０Ｈｚ）
電極先端径：６ｍｍφ
電極形状：ドーム型
【００２２】
（評価基準）
○：連続打点３０００点以上
△：連続打点１０００点以上〜３０００点未満
×：連続打点１０００点未満
評価結果を表４、５、６にあわせて示す。
【００２３】
Ｎｏ．１、４、７、２２、２７、２８、３０、３３、４８、５３、６１、６７、７２はめっき層表面から５μｍまでのＦｅの平均濃度が本発明の範囲外であるため、めっき層表面の溶融が促進されて電極寿命が短くなり、溶接性が低下した。Ｎｏ．２４、５０はめっき層表面から５μｍまでのＦｅの平均濃度が本発明の範囲内であるが、めっき層表面から５μｍまでのＳｉの平均濃度が本発明の範囲外であるため、めっき層表面の電気抵抗が高く電極寿命が短くなり、溶接性が低下した。他の実験については、本発明の範囲内の金属間化合物層をめっき層に持つアルミニウムめっき鋼板、もしくはアルミニウムめっき鋼板を使用した部品であるため、電極寿命が長く、良好な溶接性を示した。
【００２４】
【表４】
【表５】
【表６】
【発明の効果】
本発明は、抵抗溶接を用いて接合されるアルミニウムめっき鋼板とアルミニウムめっき鋼板を用いて加工された部品について、良好な溶接性をもたらすものであり、産業上の寄与は大きい。[0001]
TECHNICAL FIELD OF THE INVENTION
The present invention relates to an aluminum-plated steel sheet joined using resistance welding typified by spot welding used for automobile parts and the like, and a part processed using the aluminum-plated steel sheet.
[0002]
[Prior art]
Many of the automotive parts using thin steel plates are joined by resistance welding typified by spot welding in a vehicle body assembly process to form a vehicle body. In recent years, the use of surface-treated steel sheets with plating on the steel sheet surface has been expanding due to the demand for improved body rust prevention performance, but surface-treated steel sheets generally have lower weldability than bare steel sheets. . As the weldability to be reduced, there are two points: (1) reduction of the appropriate welding current range, and (2) reduction of the electrode life. In the former case, the current-carrying area increases as the plating metal melts, and the current and current-carrying cycle required to obtain a sufficient nugget become larger than that of a bare steel sheet, but the dust generation current and welding current increase in the nugget formation current. Instead, the proper welding current range is reduced as a result. In the latter, a copper alloy and a plating metal used as an electrode react during welding to form an alloy layer, and the electrode surface is covered with the alloy layer to deteriorate welding quality.
[0003]
In spot welding, a phenomenon is observed in which the electrode tip diameter increases, the current density decreases, and no nugget is formed. Also, in seam welding and projection welding, the shape and resistance of the electrode surface become non-uniform due to the alloy layer, and the energization is biased, and the generation of dust and the shape of the nugget deteriorate, resulting in a decrease in bonding strength and perforation. And other problems. To improve this property, (1) suppress the alloying reaction by the barrier effect of the film, and (2) reduce the alloying reaction on the electrode surface by reducing the resistance during welding under the film and welding conditions. Suppression.
[0004]
Among the plated steel sheets, the aluminum-plated steel sheet has a remarkable reaction with the copper alloy of the electrode, and is a type of steel sheet that shortens the electrode life during welding. Techniques for improving the electrode life of this aluminum-plated steel sheet include aluminum-plated steel sheets as disclosed in JP-A-10-183368, JP-A-10-46358, and JP-A-10-330957. There is a method in which a post-treatment film is applied to the surface of the electrode to improve the life of the electrode. However, the electrode life obtained with these techniques was shorter than that of bare steel plates.
[0005]
[Problems to be solved by the invention]
The present invention solves the above-mentioned problem of weldability, and provides an aluminum-plated steel sheet excellent in resistance weldability and a processed part using the same.
[0006]
[Means for Solving the Problems]
The present inventors have conducted basic studies to solve the above-mentioned problems. As a result, it has been found that by optimizing the Fe concentration and the Si concentration on the surface of the plating layer, an aluminum-plated steel sheet excellent in resistance weldability and a processed part using the same can be manufactured. That is, the alloying of the plating metal and the copper alloy as the electrode is promoted by the melting of the plating metal due to heat generation and an increase in reactivity, but increases the Fe concentration on the surface of the aluminum plating layer to increase the melting point. Thereby, it is considered that melting of the plating surface is suppressed and alloying is significantly suppressed.
[0007]
In addition, Si is usually added to an aluminum-plated steel sheet in order to suppress the growth of an Fe-Al alloy layer that lowers workability, but Si is an element that increases electric resistance, and Joule on the electrode surface is increased. It is conceivable that heat generation is promoted to adversely affect the electrode life. The present inventors have found that the Si concentration is reduced in order to reduce the electric resistance of the plating layer.
[0008]
Japanese Patent Application Laid-Open Nos. 60-251267 and 2000-38640 disclose a technique of heating an aluminum-plated steel sheet to form a plating layer of an Fe-Al alloy. The technology is not mentioned. Japanese Patent Application Laid-Open No. 9-118970 discloses a technique of heat-treating an aluminum-plated steel sheet from the viewpoint of heat resistance. However, this is a technical idea of suppressing the diffusion of Fe into a plating layer. There is no disclosure of the concentration.
[0009]
The gist of the present invention is as follows.
(1) The steel sheet has an intermetallic compound layer mainly composed of Fe and Al on the surface of the steel sheet. The average concentration of Fe up to 5 μm from the surface of the intermetallic compound layer is 30% or more by mass% and the average concentration of Si. Is 6% or less of the amount of added Si.
(2) A machined part using an aluminum-plated steel sheet excellent in resistance weldability, characterized by using the aluminum-plated steel sheet according to (1).
[0010]
BEST MODE FOR CARRYING OUT THE INVENTION
Hereinafter, the limitation range of the present invention will be described in detail.
The reason why the average concentration of Fe up to 5 μm from the surface of the intermetallic compound layer is set to 30% or more is that if the Fe concentration is less than this, the melting point of the plating layer surface does not sufficiently increase, and the plating layer surface during resistance welding does not increase. This is because the plating metal is likely to be alloyed with the copper alloy as the electrode material by melting, and the life of the electrode is shortened. The electrode life is good when the average concentration of Fe is 30% or more, but desirably the characteristics are sufficient when it is 40% or more.
[0011]
The reason why the average concentration of Si up to 5 μm from the surface of the intermetallic compound layer is 6% or less is that if the Si concentration exceeds 6%, the electrical resistance of the plating surface increases and the electrode life is shortened. The average concentration of Fe and the average concentration of Si up to a depth of 5 μm from the surface are defined as the average concentration up to a depth beyond this, and the important concentration of Fe and Si at the outermost surface is reflected. Because it is not done.
[0012]
Parts processed from a steel sheet having the above-mentioned intermetallic compound layer, and parts formed from the above-mentioned intermetallic compound layer by hot pressing or the like while the steel sheet is heated to a high temperature, have a melting surface of the plating layer during resistance welding. This suppresses alloying between the plating metal and the electrode, and suppresses heat generation due to the low electric resistance of the plating layer surface, thereby exhibiting an excellent electrode life. The chemical composition and microstructure of the steel sheet are not particularly limited. However, if the steel sheet has the above-mentioned plating layer of the intermetallic compound layer, an excellent electrode life is exhibited.
[0013]
The plating layer has a configuration in which Al is a main component and Si is added. Other additional elements include Cr, Mg, Ti, Sb, Sn, Zn, and the like, but are applicable as long as the plating layer is mainly composed of Al. However, Zn has a low boiling point, and when added in a large amount, powdered Zn is generated on the surface during heating to cause galling at the time of pressing. Therefore, addition of 60% or more is not desirable.
In the present invention, the adhesion amount of aluminum plating, pre-plating treatment, and post-treatment are not particularly limited. There is no problem at all when the amount of plating applied is in the range of 30 to 100 g / m 2 on one side.
[0014]
As the post-plating treatment, there may be a chromate treatment, a resin coating treatment, etc. for the purpose of primary rust prevention and lubricity, but the organic resin is undesirably lost when heated. In consideration of recent hexavalent chromium regulations, a chromate treatment is preferably a trivalent treatment film such as electrolytic chromate.
The method for producing the aluminum-plated steel sheet is not limited at all. Normal steelmaking and hot rolling conditions can be applied. The aluminum plating is usually performed by a hot-dip plating method, but is not limited thereto, and electroplating from a non-aqueous solvent, vapor deposition, or the like can also be used. Pre-plating such as Ni pre-plating may be used as a pre-plating process, but this is also applicable.
[0015]
The means for realizing the plating layer of the present invention is not particularly limited, but if the range of the present invention is satisfied, an excellent electrode life is exhibited. As a conceivable method, it is conceivable that a steel sheet is heated at a high temperature and an intermetallic compound layer satisfying the present invention is used as a plating layer. Absent. The composition of the surface can be controlled by changing the heat treatment conditions. As a method for measuring the surface composition of the intermetallic compound, an electron beam microanalyzer (EPMA) or an energy dispersive X-ray spectrometer (EDX) is preferable in terms of accuracy.
[0016]
【Example】
Hereinafter, examples of the present invention will be described.
Hot-rolled aluminum plating was performed using a cold-rolled steel plate (sheet thickness: 1.2 mm) having a steel composition as shown in Table 1 after normal hot rolling and cold rolling processes. Molten aluminum plating a non-oxidizing furnace - using reductive types of lines, the coating weight in plating after gas wiping method was adjusted on both sides 80 g / m 2 and 120 g / m 2, then cooled and subjected to a zero spangle treatment . Table 2 shows the plating bath composition at this time. The Fe in the bath is inevitable supplied from plating equipment and strips in the bath. The plating appearance was good without any non-plating. After plating, post-treatments shown in Table 3 were performed in-line, and skin-pass rolling was performed in-line at a rolling reduction of 0.8%.
[0017]
[Table 1]
[Table 2]
[Table 3]
The aluminum-plated steel sheet obtained in the above steps was heat-treated. The heat treatment conditions and methods are shown in Tables 4, 5, and 6. Some samples were heated and then hot pressed. Tables 4, 5, and 6 show the results of the hot-pressing experiments with the legend ○. Some of the samples were processed after cooling. The experiments performed after cooling are shown in Tables 4, 5 and 6 by the legend ○. The Fe and Si concentrations on the surface up to 5 μm were measured by an electron beam analyzer and are shown in Tables 4, 5 and 6.
[0021]
A welding test was performed on the obtained sample to examine the electrode life. The resistance welding used was spot welding, and their conditions are shown below. The evaluation was made as the number of continuous hits until the nugget diameter fell below 4 at. Welding evaluation was performed on the hot-pressed part for the experiment in which hot pressing was performed, the processed part for the experiment performed after cooling, and the steel plate for the other parts.
(Welding conditions)
Welding power source: Single-phase AC welding current: 95% of current generated by dust
Pressure: 300kgf
Welding time: 12 cycles (frequency: 60 Hz)
Electrode tip diameter: 6mmφ
Electrode shape: dome type
(Evaluation criteria)
：: continuous hit points of 3000 points or more Δ: continuous hit points of 1000 points or more to less than 3000 points x: continuous hit points of less than 1000 points The evaluation results are shown in Tables 4, 5 and 6.
[0023]
No. 1,4,7,22,27,28,30,33,48,53,61,67,72, the average concentration of Fe up to 5 μm from the plating layer surface is out of the range of the present invention. , And the life of the electrode was shortened, and the weldability was reduced. No. In Nos. 24 and 50, the average concentration of Fe up to 5 μm from the plating layer surface is within the range of the present invention, but the average concentration of Si up to 5 μm from the plating layer surface is outside the range of the present invention. The electrical resistance was high, the electrode life was short, and the weldability was low. In other experiments, since the aluminum-plated steel sheet having the intermetallic compound layer in the plating layer within the scope of the present invention or a component using the aluminum-plated steel sheet, the electrode life was long and good weldability was exhibited.
[0024]
[Table 4]
[Table 5]
[Table 6]
【The invention's effect】
INDUSTRIAL APPLICABILITY The present invention provides good weldability for an aluminum-plated steel sheet joined using resistance welding and a part processed using the aluminum-plated steel sheet, and has a great industrial contribution.
Claims (2)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002160168A JP2004002933A (en) | 2002-05-31 | 2002-05-31 | Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the aluminum plated steel sheet |
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| Application Number | Priority Date | Filing Date | Title |
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| JP2002160168A JP2004002933A (en) | 2002-05-31 | 2002-05-31 | Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the aluminum plated steel sheet |
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| JP2004002933A true JP2004002933A (en) | 2004-01-08 |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007308742A (en) * | 2006-05-17 | 2007-11-29 | Nissan Motor Co Ltd | High-tensile strength steel plate for resistance welding and joining method therefor |
| JP2008260967A (en) * | 2007-04-10 | 2008-10-30 | Nippon Steel Corp | Automobile member having excellent corrosion resistance in joint part |
| JP2012041610A (en) * | 2010-08-20 | 2012-03-01 | Jfe Steel Corp | Steel sheet for hot pressing, manufacturing method therefor and method for manufacturing hot press member |
| JP6432717B1 (en) * | 2018-05-17 | 2018-12-05 | 新日鐵住金株式会社 | Al-based plated steel sheet and manufacturing method thereof |
-
2002
- 2002-05-31 JP JP2002160168A patent/JP2004002933A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007308742A (en) * | 2006-05-17 | 2007-11-29 | Nissan Motor Co Ltd | High-tensile strength steel plate for resistance welding and joining method therefor |
| JP2008260967A (en) * | 2007-04-10 | 2008-10-30 | Nippon Steel Corp | Automobile member having excellent corrosion resistance in joint part |
| JP2012041610A (en) * | 2010-08-20 | 2012-03-01 | Jfe Steel Corp | Steel sheet for hot pressing, manufacturing method therefor and method for manufacturing hot press member |
| JP6432717B1 (en) * | 2018-05-17 | 2018-12-05 | 新日鐵住金株式会社 | Al-based plated steel sheet and manufacturing method thereof |
| WO2019220592A1 (en) * | 2018-05-17 | 2019-11-21 | 日本製鉄株式会社 | Al plated steel sheet and production method therefor |
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