JP2001355052A - Hot dip zinc-aluminum alloy plated steel sheet excellent in spot weldability and its production method - Google Patents
Hot dip zinc-aluminum alloy plated steel sheet excellent in spot weldability and its production methodInfo
- Publication number
- JP2001355052A JP2001355052A JP2001111341A JP2001111341A JP2001355052A JP 2001355052 A JP2001355052 A JP 2001355052A JP 2001111341 A JP2001111341 A JP 2001111341A JP 2001111341 A JP2001111341 A JP 2001111341A JP 2001355052 A JP2001355052 A JP 2001355052A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- aluminum alloy
- plating
- plated steel
- spot weldability
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
- C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
- C23C28/322—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer only coatings of metal elements only
- C23C28/3225—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer only coatings of metal elements only with at least one zinc-based layer
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
- C23C28/32—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer
- C23C28/321—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one pure metallic layer with at least one metal alloy layer
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C28/00—Coating for obtaining at least two superposed coatings either by methods not provided for in a single one of groups C23C2/00 - C23C26/00 or by combinations of methods provided for in subclasses C23C and C25C or C25D
- C23C28/30—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer
- C23C28/34—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates
- C23C28/345—Coatings combining at least one metallic layer and at least one inorganic non-metallic layer including at least one inorganic non-metallic material layer, e.g. metal carbide, nitride, boride, silicide layer and their mixtures, enamels, phosphates and sulphates with at least one oxide layer
Abstract
Description
【0001】[0001]
【発明の属する技術分野】本発明は、スポット溶接性に
優れた溶融亜鉛−アルミニウム合金めっき鋼板とその製
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 zinc-aluminum alloy-coated steel sheet having excellent spot weldability and a method for producing the same.
【0002】[0002]
【従来の技術】近年、自動車、家庭電気製品、建材等の
耐用年数の長期化に対応するため、表面処理鋼板の使用
が拡大している。特にZn−5%Al溶融めっき鋼板
は、今までの溶融亜鉛めっきに比較して耐食性が優れて
いることから、建材などを中心に使用されている。ま
た、最近ではZn−Al−Mg系めっき鋼板が開発され
てきており、さらなる耐食性の向上が図られてきてい
る。2. Description of the Related Art In recent years, the use of surface-treated steel sheets has been expanding in order to cope with prolonged service life of automobiles, household electric appliances, building materials and the like. Particularly, Zn-5% Al hot-dip galvanized steel sheet is used mainly for building materials and the like because of its excellent corrosion resistance as compared with conventional hot-dip galvanized steel sheet. In recent years, Zn—Al—Mg plated steel sheets have been developed, and further improvement in corrosion resistance has been attempted.
【0003】しかしこのようなZn−高Al系合金めっ
き鋼板には溶接性が劣っているという欠点がある。これ
は溶融亜鉛めっきの融点が約419℃であるのに対し、
高Al系合金めっき鋼板の融点が一般に低くスポット溶
接時にめっき層が容易に溶解して溶接部の接触面積が大
きくなり電流密度が低下し、ナゲット径が小さくなると
共にCu−Zn合金が生成し電極が損耗するのである。
このため溶接チップ表面の加熱が過大となり電極チップ
表面に脆い合金層が堆積しチップ損耗が激しくなるとい
う欠点もあり改善が求められている。[0003] However, such a Zn-high Al-based alloy-plated steel sheet has a drawback of poor weldability. This is because the melting point of hot-dip galvanizing is about 419 ° C,
The melting point of a high Al alloy plated steel sheet is generally low, and the plating layer is easily melted during spot welding to increase the contact area of the welded part, reduce the current density, decrease the nugget diameter, and generate a Cu-Zn alloy to form an electrode. Is worn out.
For this reason, there is a disadvantage that heating of the surface of the welding tip is excessive, a brittle alloy layer is deposited on the surface of the electrode tip, and chip wear becomes severe.
【0004】合金化溶融亜鉛めっき鋼板における溶接性
を向上させる方法として特開平2-4983号公報にZ
nOを主成分とする酸化皮膜を形成させる技術が開示さ
れているが、工業的にZnO皮膜を容易に形成させるこ
とが困難であり、実用化に至っていない。また、特開平
5−263210号公報にはZn−5%Al系合金めっ
き鋼板にFeの合金化を促進するTiを添加し、めっき
後に合金化炉を使用してFeを合金化させ、スポット溶
接性を改善させる技術が記載されている。しかし、これ
は合金化炉が必須であり高コストとなるという問題があ
る。また、特開平6−336664号公報には亜鉛−ア
ルミニウム系溶融めっき浴に鋼板を浸漬後珪素含有水溶
液を噴霧してめっき表面にシリカ被膜を形成しスポット
溶接性を改善する技術が記載されているが、これはシリ
カ被膜を鋼板上に密着性良く一様に形成することが困難
であり、現状ではあまり効果がないという問題がある。As a method of improving the weldability of an alloyed hot-dip galvanized steel sheet, Japanese Patent Application Laid-Open No. 2-4983 discloses Z
Although a technique for forming an oxide film containing nO as a main component is disclosed, it is difficult to easily form a ZnO film industrially, and it has not been put to practical use. Japanese Patent Application Laid-Open No. 5-263210 discloses the addition of Ti to promote the alloying of Fe to a Zn-5% Al-based alloy-plated steel sheet, and after plating, alloying the Fe using an alloying furnace and spot welding. A technique for improving the performance is described. However, this has a problem that an alloying furnace is indispensable and the cost is high. JP-A-6-336664 describes a technique for improving the spot weldability by immersing a steel sheet in a zinc-aluminum hot-dip bath and spraying a silicon-containing aqueous solution to form a silica coating on the plating surface. However, it is difficult to uniformly form a silica coating on a steel sheet with good adhesion, and there is a problem that it is not very effective at present.
【0005】[0005]
【発明が解決しようとする課題】このような状況に鑑
み、従来の亜鉛−アルミニウム系合金めっき鋼板のスポ
ット溶接性を改善した溶融亜鉛-アルミニウム系合金め
っき鋼板を提供することが本発明の目的である。In view of such circumstances, it is an object of the present invention to provide a hot-dip zinc-aluminum-based alloy-coated steel sheet having improved spot weldability of a conventional zinc-aluminum-based alloy-coated steel sheet. is there.
【0006】[0006]
【課題を解決するための手段】スポット溶接性の劣化は
めっき合金の融点低下と電極上でのCu−Zn合金生成
による電極の損耗で起こること、めっき後の後処理によ
るめっき浴表層のみの改質では溶接性能のばらつきが大
きいとの認識に基づき、本発明者らは、めっき合金の組
成及び構造を変えることを指向した。そして鋭意検討の
結果、めっき浴中にSiを添加することが有効あること
を突き止めた。この理由は明らかではないが、Siが
Cu−Zn合金生成を抑制すること、SiがAl系酸
化物の生成を抑制することが影響しているものと考えら
れる。また、本発明者らはめっき層中のSiの存在状態
を調査したところ、金属Si、SiO2、Mg2Si等多
岐にわたり、必ずしもシリカの存在によらないことを知
見した。さらに詳細な調査を行ったところ、めっき層中
のSi系物質のサイズが大きい場合、スポット溶接性が
劣化し、その数が多くなると顕著に劣化してくることを
突き止めた。本発明はこれらの知見に基づきなされたも
ので、その要旨とするところは、以下に示す通りであ
る。The deterioration of the spot weldability is caused by the lowering of the melting point of the plating alloy and the wear of the electrode due to the formation of a Cu-Zn alloy on the electrode. Based on the recognition that there is a large variation in welding performance in quality, the present inventors aimed to change the composition and structure of the plated alloy. As a result of intensive studies, they have found that it is effective to add Si into the plating bath. Although the reason is not clear, it is considered that Si suppresses the formation of the Cu—Zn alloy and that Si suppresses the formation of the Al-based oxide. Further, the present inventors have investigated the existence state of Si in the plating layer, and found that it is not necessarily due to the presence of silica in a wide variety of areas such as metal Si, SiO 2 , and Mg 2 Si. As a result of a more detailed investigation, it was found that when the size of the Si-based material in the plating layer was large, the spot weldability was deteriorated, and when the number was large, the spot weldability was significantly deteriorated. The present invention has been made based on these findings, and the gist thereof is as follows.
【0007】(1) 鋼板の表面に質量%でAl:3〜
20%、Si:0.01〜2%を含み、残部Zn及び不
可避的不純物とからなるめっき層を有し、100μm2
以上の面積のSi系物質をめっき層の単位断面積当たり
6×103個以下含有することを特徴とするスポット溶
接性に優れた溶融亜鉛−アルミニウム合金めっき鋼板。(1) Al: 3% by mass% on the surface of the steel sheet
20%, contains Si: 0.01 to 2%, has a plating layer composed of Zn and inevitable impurities, and has a thickness of 100 μm 2.
A hot-dip zinc-aluminum alloy-plated steel sheet having excellent spot weldability, comprising not more than 6 × 10 3 Si-based substances per unit cross-sectional area of a plating layer.
【0008】(2) 上記(1)に記載のめっき鋼板の
めっき層中にさらに、Mg:0.1〜10%を含有する
ことを特徴とするスポット溶接性に優れた溶融亜鉛−ア
ルミニウム合金めっき鋼板。(2) Hot-dip zinc-aluminum alloy plating excellent in spot weldability, characterized in that the plated layer of the plated steel sheet according to (1) further contains Mg: 0.1 to 10%. steel sheet.
【0009】(3) 上記(1)または(2)記載のめ
っき鋼板のめっき層中にさらに、Ti、Cr、Ni、S
nの1種以上を質量%で0.01〜2%含有することを
特徴とするスポット溶接性に優れた溶融亜鉛−アルミニ
ウム合金めっき鋼板。(3) The plating layer of the plated steel sheet according to (1) or (2) further contains Ti, Cr, Ni, S
A hot-dip zinc-aluminum alloy-plated steel sheet having excellent spot weldability, characterized by containing at least one kind of n in an amount of 0.01 to 2% by mass%.
【0010】(4) 上記(1)乃至(3)のいずれか
に記載のめっき鋼板のめっき層の上に、無機酸化物皮膜
を70mg/m2〜2g/m2有することを特徴とするス
ポット溶接性に優れた溶融亜鉛−アルミニウム合金めっ
き鋼板。(4) A spot characterized by having an inorganic oxide film of 70 mg / m 2 to 2 g / m 2 on the plated layer of the plated steel sheet according to any one of (1) to (3). Hot-dip zinc-aluminum alloy plated steel sheet with excellent weldability.
【0011】(5)上記(1)乃至(3)のいずれかに
記載のめっき鋼板のめっき層の上に、有機樹脂皮膜を1
00mg/m2〜2g/m2有することを特徴とするスポ
ット溶接性に優れた溶融亜鉛−アルミニウム合金めっき
鋼板。(5) An organic resin film is formed on the plated layer of the plated steel sheet according to any of (1) to (3) above.
A hot-dip zinc-aluminum alloy-plated steel sheet having excellent spot weldability, having a content of from 00 mg / m 2 to 2 g / m 2 .
【0012】(6) 溶融亜鉛−アルミニウム合金めっ
き鋼板を製造するに際し、めっき浴温を400℃以上と
することにより、めっき層中に100μm2以上の面積
のSi系物質をめっき層の単位断面積当たり6×103
個以下含有させることを特徴とする上記(1)乃至
(5)のいずれかに記載のスポット溶接性に優れた溶融
亜鉛−アルミニウム合金めっき鋼板の製造方法。(6) When manufacturing a hot-dip zinc-aluminum alloy-plated steel sheet, the plating bath temperature is set to 400 ° C. or more, so that the Si-based material having an area of 100 μm 2 or more in the plated layer has a unit sectional area of the plated layer. 6 × 10 3 per
The method for producing a hot-dip zinc-aluminum alloy-coated steel sheet excellent in spot weldability according to any one of the above (1) to (5), wherein the steel sheet contains not more than one steel sheet.
【0013】[0013]
【発明の実施の形態】以下、本発明を詳細に説明する。
まずめっき層中に含有させる元素について説明する。BEST MODE FOR CARRYING OUT THE INVENTION Hereinafter, the present invention will be described in detail.
First, the elements contained in the plating layer will be described.
【0014】めっき層中のAlは耐食性の向上のために
添加される。3%未満では耐食性が劣り、20%を超え
ると耐食性向上効果が飽和すると共にスポット溶接性が
劣化するため3〜20%とした。Al in the plating layer is added for improving corrosion resistance. If it is less than 3%, the corrosion resistance is inferior. If it exceeds 20%, the effect of improving the corrosion resistance is saturated and the spot weldability is deteriorated, so that the content is set to 3 to 20%.
【0015】Siは本発明にとり重要な元素であり、ス
ポット溶接性の向上のために添加する。0.01%未満
では、スポット溶接性の向上が見られず2%を超えると
スポット溶接性が劣化するため0.01〜2%とする。Si is an important element in the present invention, and is added for improving spot weldability. If it is less than 0.01%, spot weldability is not improved, and if it exceeds 2%, spot weldability deteriorates, so the content is made 0.01 to 2%.
【0016】Si系物質(金属Si、SiO2、Mg2S
i等)のめっき層中のサイズについては、100μm2
を超えるものがある場合にはミクロ的に抵抗に差異が生
じスポット溶接時に爆飛が発生し易くなり、スポット溶
接性が劣化する傾向にある。そして、このサイズ以上の
Si系物質がめっき層の単位断面積当たり6×103個
を超えると、スポット溶接性が顕著に劣化するため、1
00μm2以上の面積のSi系物質の個数をめっき層の
単位断面積当たり6×103個以下とした。Si-based materials (metallic Si, SiO 2 , Mg 2 S
i) etc. for the size in the plating layer is 100 μm 2
If some of them exceed the above, a difference in resistance microscopically occurs, explosion tends to occur during spot welding, and the spot weldability tends to deteriorate. If the Si-based substance having a size of not less than 6 × 10 3 per unit sectional area of the plating layer, the spot weldability is remarkably deteriorated.
The number of Si-based materials having an area of 00 μm 2 or more was set to 6 × 10 3 or less per unit sectional area of the plating layer.
【0017】Mgは一般には耐食性向上効果があること
から添加されることが多いが本発明ではMg添加により
溶接性に悪影響を及ぼすAl2O3の生成を抑制すること
で溶接性の劣化を抑制する。0.1%未満では添加効果
がなく、10%を超えると浴ドロスの発生が多く、めっ
きが困難になるため0.1〜10%としたが、好ましく
は0.5〜10%である。In general, Mg is often added because it has an effect of improving corrosion resistance. However, in the present invention, deterioration of weldability is suppressed by suppressing the generation of Al 2 O 3 that adversely affects weldability by adding Mg. I do. If it is less than 0.1%, there is no effect of addition, and if it exceeds 10%, bath dross often occurs and plating becomes difficult. Therefore, the content is set to 0.1 to 10%, preferably 0.5 to 10%.
【0018】Ti、Cr、Ni及びSnは溶接性の安定
化のために必要に応じて添加される。0.01%未満で
は添加効果がなく、2%を超えると溶接性向上効果が飽
和するため0.01〜2%とする。[0018] Ti, Cr, Ni and Sn are added as necessary to stabilize the weldability. If it is less than 0.01%, there is no effect of addition, and if it exceeds 2%, the effect of improving the weldability is saturated.
【0019】使用するめっき原板には特に限定はなく、
製鋼方法や鋼の強度、熱延PO材、冷延材等製品によら
ず使用可能である。めっきは、ゼンジミアタイプ、フラ
ックスタイプ、または、プレめっきタイプ等の製造方法
によらず、本技術は適用可能である。There is no particular limitation on the plating base plate to be used.
It can be used regardless of the steelmaking method, the strength of the steel, hot rolled PO material, cold rolled material, and other products. The present technology can be applied to plating without depending on a manufacturing method such as a Sendzimir type, a flux type, or a pre-plating type.
【0020】めっき浴温は浴へのSiの均一分散性に影
響を与え、400℃未満ではSiの析出が起こり、Si
系物質が粗大になり過ぎ、溶接性を阻害するようにな
る。また、めっき浴がドロスアウトし易くなり釜歩留り
の低下につながるため400℃以上とする。The plating bath temperature affects the uniform dispersibility of Si in the bath. If the temperature is lower than 400 ° C., precipitation of Si occurs,
The system material becomes too coarse, which impairs weldability. In addition, the temperature is set to 400 ° C. or more because the plating bath tends to dross out, which leads to a decrease in the yield of the pot.
【0021】また、耐黒変性、耐食性向上のためにめっ
き後に水系、有機系後処理を施しても特に問題なく、調
質圧延を行ってもかまわない。In order to improve the blackening resistance and the corrosion resistance, an aqueous or organic post-treatment may be performed after the plating without any problem, and the temper rolling may be performed.
【0022】めっき後のめっき層上に、更にSi、M
g、Zr、Mo、Ce、Caの酸化物から選ばれる少な
くとも1種以上の無機酸化物を被覆させると本発明の効
果をより一層向上させることができる。この場合、例え
ばりん酸塩等の複合酸化物とすることも何等問題はな
い。この無機酸化物皮膜の被覆量が70mg/m2未満
では溶接性の向上効果が十分ではなく、また、2g/m
2を超えると不通電し易くなり溶接性が劣化するため、
無機酸化物皮膜の被覆量は70mg/m2〜2g/m2と
した。On the plated layer after plating, further add Si, M
The effect of the present invention can be further improved by coating at least one or more inorganic oxides selected from g, Zr, Mo, Ce and Ca oxides. In this case, there is no problem in forming a composite oxide such as a phosphate. If the coating amount of the inorganic oxide film is less than 70 mg / m 2 , the effect of improving the weldability is not sufficient, and 2 g / m 2
If it exceeds 2 , it becomes easy to de-energize and the weldability deteriorates.
The coating amount of the inorganic oxide film was 70 mg / m 2 to 2 g / m 2 .
【0023】また、この無機酸化物皮膜の代わりに有機
樹脂皮膜を被覆させても、無機酸化物皮膜と同様に本発
明の効果をより一層向上させることができる。100m
g/m2未満では溶接性の向上効果が十分ではなく、2
g/m2を超えると不通電し易くなり溶接性が劣化する
ため、有機樹脂皮膜の被覆量は100mg/m2〜2g
/m2とした。有機樹脂としては、水系樹脂、溶剤系樹
脂、粉体系樹脂、無溶剤系樹脂のどのような形態でも良
い。ここでいう水系樹脂とは水溶性樹脂の他、本来水不
溶性でありながらエマルジョンやサスペンジョンのよう
に水不溶性樹脂が水中に微分散された状態になり得るも
の(水分散性樹脂)を含めていう。Further, even when an organic resin film is coated instead of the inorganic oxide film, the effect of the present invention can be further improved similarly to the case of the inorganic oxide film. 100m
If less than g / m 2 , the effect of improving weldability is not sufficient,
If it exceeds g / m 2 , it becomes easy to conduct electricity and the weldability deteriorates. Therefore, the coating amount of the organic resin film is 100 mg / m 2 to 2 g.
/ M 2 . The organic resin may be in any form of a water-based resin, a solvent-based resin, a powder-based resin, or a non-solvent-based resin. The term "aqueous resin" used herein includes not only a water-soluble resin but also a resin (a water-dispersible resin) which is inherently water-insoluble but can be finely dispersed in water, such as an emulsion or a suspension.
【0024】有機樹脂として使用できる樹脂は、特に限
定しないが、ポリオレフィン系樹脂、アクリルオレフィ
ン系樹脂、ポリウレタン系樹脂、アクリル系樹脂、ポリ
カーボネート系樹脂、エポキシ系樹脂、ポリエステル系
樹脂、アルキド系樹脂、フェノール系樹脂、その他の加
熱硬化型の樹脂などが挙げられ、架橋可能なものがより
好ましい。有機樹脂は2種類以上を混合して使用しても
良いし、或いは共重合させて使用しても良い。また、必
要に応じて各種メラミン樹脂、アミノ樹脂等の架橋剤を
添加しても良い。これらの中で特に、性能面とコスト面
の両立を考慮する場合はアクリルオレフィン系樹脂、ア
クリル系樹脂を用いるのが望ましい。さらに、有機樹脂
に加えて微粒シリカや潤滑剤を少量添加しても本発明の
効果を損なうことはない。The resin that can be used as the organic resin is not particularly limited, but includes polyolefin resin, acrylic olefin resin, polyurethane resin, acrylic resin, polycarbonate resin, epoxy resin, polyester resin, alkyd resin, and phenol. Examples include a base resin and other heat-curable resins, and a crosslinkable resin is more preferable. The organic resin may be used as a mixture of two or more kinds, or may be used after being copolymerized. Further, a crosslinking agent such as various melamine resins and amino resins may be added as needed. Among these, it is particularly preferable to use an acrylic olefin resin or an acrylic resin when considering both the performance and the cost. Furthermore, the effect of the present invention is not impaired even if a small amount of fine silica or a lubricant is added in addition to the organic resin.
【0025】無機酸化物皮膜或いは有機樹脂皮膜を形成
させるための塗布方法としては、スプレー、カーテンコ
ート、フローコーター、ロールコーター、バーコータ
ー、刷毛塗り、浸漬及びエアナイフ絞り等のいずれの方
法も適用できる。また到達焼付け温度は80〜250℃
とするのが望ましい。80℃未満では塗料中の水が完全
に揮発しづらいため耐食性が低下するなどの悪影響を及
ぼす。250℃を超えると有機物である樹脂のアルキル
部分が熱分解等の変性を起こしたり、皮膜の硬化が進み
すぎて耐食性や加工性が低下したりするため好ましくな
い。より好ましくは80〜160℃である。また、乾燥
設備については特に限定しないが、熱風吹き付けによる
方法や、ヒーターによる間接加熱方法、赤外線による方
法、誘導加熱による方法、並びにこれらを併用する方法
も採用できる。また、使用する有機樹脂の種類によって
は、紫外線や電子線などのエネルギー線によって硬化さ
せることもできる。As a coating method for forming an inorganic oxide film or an organic resin film, any method such as spraying, curtain coating, flow coater, roll coater, bar coater, brush coating, dipping, and air knife drawing can be applied. . The baking temperature is 80-250 ° C
It is desirable that If the temperature is lower than 80 ° C., water in the paint is difficult to completely volatilize, which has an adverse effect such as a decrease in corrosion resistance. If the temperature is higher than 250 ° C., the alkyl portion of the organic resin is undesirably denatured by thermal decomposition or the like, or the curing of the film is excessively advanced and the corrosion resistance and workability are lowered. More preferably, it is 80 to 160 ° C. The drying equipment is not particularly limited, but a method using hot air blowing, an indirect heating method using a heater, a method using infrared rays, a method using induction heating, and a method using these in combination can also be adopted. In addition, depending on the type of the organic resin used, the resin can be cured by energy rays such as ultraviolet rays and electron beams.
【0026】[0026]
【実施例】(実施例1)鋼スラブを溶製して通常の方法
で薄鋼板を製造した板厚0.8mmのSPCC板をめっ
き原板とした。めっきはゼンジミアタイプの連続溶融亜
鉛めっきラインにて加熱、焼鈍、めっきを行った。焼鈍
雰囲気は、10%水素、残90%窒素ガス雰囲気であ
り、露点を−30度とした。焼鈍温度は730℃、焼鈍
時間は3分である。めっき浴はAl:3.5〜21%、
Mg:0〜10.5%、Si:0〜2.2%、Ti:0
〜1.8%、Cr:0〜1.7%、Ni:0〜1.7
%、Sn:0.4〜1.8%、残部Zn及び不可避的不
純物に調整しためっき浴を使用した。得られためっき鋼
板の組成を表1に示す。めっき浴温は390〜500℃
で行い、めっき後は通常のワイピングによりめっき付着
量を片面当たり90g/m2に調整した。めっき後、調
質圧延を1%行い、その後、必要に応じてクロメート処
理を20〜30mg/m2の付着量で実施した。このよ
うに製造されためっき鋼板のSi系物質については、め
っき断面のEPMA観察を実施し、任意の100μm平
方の視野毎に観察し、100μm2以上のものの個数を
数え、めっき層断面の単位断面積当たりの個数として表
した。結果を表1に示す。EXAMPLES (Example 1) A 0.8 mm-thick SPCC plate produced by melting a steel slab and producing a thin steel plate by a usual method was used as a plating original plate. The plating was performed by heating, annealing and plating in a Sendzimir-type continuous hot-dip galvanizing line. The annealing atmosphere was a 10% hydrogen, 90% remaining nitrogen gas atmosphere, and the dew point was -30 degrees. The annealing temperature is 730 ° C. and the annealing time is 3 minutes. The plating bath is Al: 3.5 to 21%,
Mg: 0 to 10.5%, Si: 0 to 2.2%, Ti: 0
To 1.8%, Cr: 0 to 1.7%, Ni: 0 to 1.7
%, Sn: 0.4 to 1.8%, and a plating bath adjusted to Zn and inevitable impurities was used. Table 1 shows the composition of the obtained plated steel sheet. Plating bath temperature is 390-500 ° C
After plating, the amount of coating was adjusted to 90 g / m 2 per one side by ordinary wiping. After plating, temper rolling was performed at 1%, and then, if necessary, chromate treatment was performed at an adhesion amount of 20 to 30 mg / m 2 . For Si-based material thus produced plated steel sheet, conducted EPMA observation of the plating section, was observed for each field of view of any of 100 [mu] m square, counts the number of 100 [mu] m 2 or more of, unit cross-sectional of the plating layer cross-section Expressed as the number per area. Table 1 shows the results.
【0027】得られためっき鋼板の溶接性の評価は、連
続打点性試験による評価と溶接安定性による評価で行っ
た。The evaluation of the weldability of the obtained plated steel sheet was carried out by an evaluation by a continuous hitting test and an evaluation by welding stability.
【0028】(連続打点性試験)めっき鋼板を2枚重ね
併せてスポット溶接の連続打点性試験を実施した。(Continuous spotting test) A continuous spotting test of spot welding was carried out by superposing two plated steel sheets.
【0029】試験条件は、電極形状:先端ドーム径12
φ、加圧力:220kgf、溶接時間:12サイクル
(AC 50サイクル)、溶接電流:12kAで行い、
剪断引張後のナゲット径を測定して、その値が4.5m
mになった時を電極寿命とした。電極寿命が2000点
以上のものを○、1000〜2000点を△、1000
点未満を×とし、△と×を不合格とした。The test conditions were as follows: electrode shape: tip dome diameter 12
φ, pressing force: 220 kgf, welding time: 12 cycles (50 cycles of AC), welding current: 12 kA,
The nugget diameter after shear tension was measured and the value was 4.5 m.
The time when the value reached m was regarded as the electrode life. When the electrode life is 2,000 points or more: ○, 1000 to 2000 points: Δ, 1000
Less than the point was marked as x, and △ and x were rejected.
【0030】(溶接安定性)電極寿命が2000点以上
のものについて、2000点から2010点までのナゲ
ット径サイズのばらつきで表し、最大と最小のナゲット
サイズの差が0.3mm以下のものを◎、0.5mm以
下のものを○とし、それぞれ合格とした。(Welding stability) For those having an electrode life of 2,000 points or more, the variation in the nugget diameter size from 2000 points to 2010 points is indicated. The difference between the maximum and minimum nugget sizes is 0.3 mm or less. , 0.5 mm or less were evaluated as ○ and passed.
【0031】評価結果を表1に示す。No.1からN
o.36は本発明例であり、溶接性は良好である。特
に、No.21〜No.36はめっき層中に、さらにT
i、Cr、Ni、或いはSnを含有させた例で、連続打
点性の他に溶接安定性にも優れたものとなっている。一
方、No.37からNo.45は比較例であり、No.
44はAlが高すぎるため溶接性に劣り、No.37、
No.38、No.40、No.41、No.42はS
i量が低すぎるため、またNo.45はSiが高すぎる
ため、さらにNo.43はMgが高すぎるため、No.
39は浴温が低すぎるためいずれも溶接性に劣る結果と
なっている。Table 1 shows the evaluation results. No. 1 to N
o. 36 is an example of the present invention, and has good weldability. In particular, no. 21-No. Reference numeral 36 denotes T in the plating layer.
This is an example in which i, Cr, Ni, or Sn is contained, and is excellent in welding stability in addition to continuous hitting property. On the other hand, No. 37 to No. 37 No. 45 is a comparative example.
No. 44 was inferior in weldability because Al was too high. 37,
No. 38, no. 40, no. 41, no. 42 is S
i amount is too low. No. 45 is No. 45 because Si is too high. No. 43 is No. 43 because Mg is too high.
Sample No. 39 was inferior in weldability because the bath temperature was too low.
【0032】[0032]
【表1】 [Table 1]
【0033】(実施例2)鋼スラブを溶製して通常の方
法で薄鋼板を製造した板厚0.8mmのSPCC板をめ
っき原板とした。めっきはゼンジミアタイプの連続溶融
亜鉛めっきラインにて加熱、焼鈍、めっきを行った。焼
鈍雰囲気は、10%水素、残90%窒素ガス雰囲気であ
り、露点を−30度とした。焼鈍温度は730℃、焼鈍
時間は3分である。めっき浴はAl:3.5〜22%、
Mg:0〜10.5%、Si:0〜2.2%、Ti:0
〜1.7%、Cr:0〜1.7%、Ni:0〜1.7
%、Sn:0〜1.9%、残部Zn及び不可避的不純物
に調整しためっき浴を使用した。得られためっき鋼板の
組成を表2に示す。めっき浴温は390〜510℃で行
い、めっき後は通常のワイピングによりめっき付着量を
片面当たり90g/m2に調整した。めっき後、調質圧
延を1%行った。その後、後処理を行った。後処理は無
機酸化物被覆処理を70mg/m2〜2500mg/m2
の範囲で行った。(Example 2) A 0.8 mm-thick SPCC plate prepared by melting a steel slab to produce a thin steel plate by a usual method was used as a plating original plate. The plating was performed by heating, annealing and plating in a Sendzimir-type continuous hot-dip galvanizing line. The annealing atmosphere was a 10% hydrogen, 90% remaining nitrogen gas atmosphere, and the dew point was -30 degrees. The annealing temperature is 730 ° C. and the annealing time is 3 minutes. The plating bath is Al: 3.5 to 22%,
Mg: 0 to 10.5%, Si: 0 to 2.2%, Ti: 0
To 1.7%, Cr: 0 to 1.7%, Ni: 0 to 1.7
%, Sn: 0 to 1.9%, a plating bath adjusted to the balance of Zn and inevitable impurities was used. Table 2 shows the composition of the obtained plated steel sheet. The plating bath temperature was 390 to 510 ° C., and after plating, the amount of coating was adjusted to 90 g / m 2 per side by ordinary wiping. After plating, temper rolling was performed at 1%. Thereafter, post-processing was performed. For post-treatment, the inorganic oxide coating treatment is performed at 70 mg / m 2 to 2500 mg / m 2.
It went in the range of.
【0034】得られためっき鋼板の溶接性の評価は、連
続打点性試験による評価と溶接安定性による評価で行っ
た。The evaluation of the weldability of the obtained plated steel sheet was carried out by an evaluation by a continuous hitting test and an evaluation by welding stability.
【0035】(連続打点性試験)めっき鋼板を2枚重ね
併せてスポット溶接の連続打点性試験を実施した。(Continuous spotting test) A continuous spotting test of spot welding was carried out by superposing two coated steel sheets.
【0036】試験条件は、電極形状:先端ドーム径12
φ、加圧力:220kgf、溶接時間:12サイクル
(AC 50サイクル)、溶接電流:12kAで行い、
剪断引張後のナゲット径を測定して、その値が4.5m
mになった時を電極寿命とした。電極寿命が2500点
超を◎、2000〜2500点を○、1000〜200
0点を△、1000点未満を×とし、△と×を不合格と
した。The test conditions were as follows: electrode shape: tip dome diameter 12
φ, pressing force: 220 kgf, welding time: 12 cycles (50 cycles of AC), welding current: 12 kA,
The nugget diameter after shear tension was measured and the value was 4.5 m.
The time when the value reached m was regarded as the electrode life. The electrode life was over 2,500 points for ◎, 2000 to 2500 points for ○, 1000 to 200
0 points were rated as △, less than 1000 points were rated as x, and × and x were rejected.
【0037】(溶接安定性)電極寿命が2000点以上
のものについて、2000点から2010点までのナゲ
ット径サイズのばらつきで表し、最大と最小のナゲット
サイズの差が0.3mm以下のものを◎、0.5mm以
下のものを○とし、それぞれ合格とした。(Welding stability) For those having an electrode life of 2,000 points or more, the variation in the nugget diameter size from 2000 points to 2010 points is shown, and the difference between the maximum and minimum nugget sizes is 0.3 mm or less. , 0.5 mm or less were evaluated as ○ and passed.
【0038】結果を表2に示す。No.46からNo.
77が本発明例で、いずれも良好な溶接性を示してい
る。No.78からNo.86は比較例であり、No.
78、No.79、No.85、No.86は無機酸化
物皮膜が厚すぎるため溶接性が劣り、No.80〜N
o.85はめっき層中の成分が本発明範囲外となってい
るため、無機皮膜処理を施しても溶接性が不十分となっ
ている。The results are shown in Table 2. No. No. 46 to No.
77 is an example of the present invention, and all show good weldability. No. No. 78 to No. No. 86 is a comparative example.
78, no. 79, no. 85, no. No. 86 was inferior in weldability because the inorganic oxide film was too thick. 80-N
o. In the case of No. 85, the components in the plating layer are out of the range of the present invention, so that even if the inorganic coating treatment is performed, the weldability is insufficient.
【0039】[0039]
【表2】 [Table 2]
【0040】(実施例3)鋼スラブを溶製して通常の方
法で薄鋼板を製造した板厚0.8mmのSPCC板をめ
っき原板とした。めっきはゼンジミアタイプの連続溶融
亜鉛めっきラインにて加熱、焼鈍、めっきを行った。焼
鈍雰囲気は、10%水素、残90%窒素ガス雰囲気であ
り、露点を−30度とした。焼鈍温度は730℃、焼鈍
時間は3分である。めっき浴の組成はAl:3.5〜2
2%、Mg:0〜10.5%、Si:0〜2.2%、T
i:0〜1.7%、Cr:0〜1.7%、Ni:0〜
1.7%、Sn:0〜1.9%、残部Zn及び不可避的
不純物に調整しためっき浴を使用した。得られためっき
鋼板の組成を表3に示す。めっき浴温は390〜510
℃で行い、めっき後は通常のワイピングによりめっき付
着量を片面当たり90g/m2に調整した。めっき後、
調質圧延を1%行い、溶剤脱脂後に表3に示す樹脂系の
有機樹脂皮膜処理を行った。Example 3 A 0.8 mm-thick SPCC plate produced by melting a steel slab to produce a thin steel plate by a usual method was used as a plating original plate. The plating was performed by heating, annealing and plating in a Sendzimir-type continuous hot-dip galvanizing line. The annealing atmosphere was a 10% hydrogen, 90% remaining nitrogen gas atmosphere, and the dew point was -30 degrees. The annealing temperature is 730 ° C. and the annealing time is 3 minutes. The composition of the plating bath is Al: 3.5-2.
2%, Mg: 0 to 10.5%, Si: 0 to 2.2%, T
i: 0 to 1.7%, Cr: 0 to 1.7%, Ni: 0 to 0%
A plating bath adjusted to 1.7%, Sn: 0 to 1.9%, the balance being Zn and unavoidable impurities was used. Table 3 shows the composition of the obtained plated steel sheet. Plating bath temperature is 390-510
C., and after plating, the coating weight was adjusted to 90 g / m 2 per side by ordinary wiping. After plating,
Temper rolling was performed at 1%, and after the solvent was degreased, a resin-based organic resin film treatment shown in Table 3 was performed.
【0041】得られためっき鋼板の溶接性の評価は、連
続打点性試験による評価と溶接安定性による評価で行っ
た。Evaluation of the weldability of the obtained plated steel sheet was performed by an evaluation by a continuous hitting test and an evaluation by welding stability.
【0042】(連続打点性試験)めっき鋼板を2枚重ね
併せてスポット溶接の連続打点性試験を実施した。(Continuous spotting test) A continuous spotting test of spot welding was performed by superposing two plated steel sheets.
【0043】試験条件は、電極形状:先端ドーム径12
φ、加圧力:220kgf、溶接時間:12サイクル
(AC 50サイクル)、溶接電流:12kAで行い、
剪断引張後のナゲット径を測定して、その値が4.5m
mになった時を電極寿命とした。電極寿命が2500点
超を◎、2000〜2500点を○、1000〜200
0点を△、1000点未満を×とし、△と×を不合格と
した。The test conditions were as follows: electrode shape: tip dome diameter 12
φ, pressing force: 220 kgf, welding time: 12 cycles (50 cycles of AC), welding current: 12 kA,
The nugget diameter after shear tension was measured and the value was 4.5 m.
The time when the value reached m was regarded as the electrode life. The electrode life was over 2,500 points for ◎, 2000 to 2500 points for ○, 1000 to 200
0 points were rated as △, less than 1000 points were rated as x, and × and x were rejected.
【0044】(溶接安定性)電極寿命が2000点以上
のものについて、2000点から2010点までのナゲ
ット径サイズのばらつきで表し、最大と最小のナゲット
サイズの差が0.3mm以下のものを◎、0.5mm以
下のものを○とし、それぞれ合格とした。(Welding stability) For those having an electrode life of 2,000 points or more, the variation in the nugget diameter size from 2000 to 2010 points is represented by ◎, where the difference between the maximum and minimum nugget sizes is 0.3 mm or less. , 0.5 mm or less were evaluated as ○ and passed.
【0045】結果を表3に示す。No.87〜No.1
32は本発明例で、いずれも良好な溶接性を示した。N
o.133とNo.134は皮膜量が少なく、溶接性向
上効果が得られておらず、No.135とNo.136
は逆に皮膜が厚すぎて溶接性が劣る結果となっている。Table 3 shows the results. No. 87-No. 1
Reference numeral 32 is an example of the present invention, and all showed good weldability. N
o. 133 and no. In the case of No. 134, the amount of the film was small and no effect of improving the weldability was obtained. 135 and no. 136
On the contrary, the result is that the film is too thick and the weldability is poor.
【0046】[0046]
【表3】 [Table 3]
【0047】[0047]
【発明の効果】このように本発明によれば、溶接性に優
れた溶融亜鉛−アルミニウム系合金めっき鋼板を製造す
ることが可能となり、自動車、建材等の産業上きわめて
大きな効果を有している。As described above, according to the present invention, it is possible to produce a hot-dip zinc-aluminum-based alloy-coated steel sheet having excellent weldability, which has an extremely great effect in industries such as automobiles and building materials. .
フロントページの続き (72)発明者 高橋 彰 君津市君津1番地 新日本製鐵株式会社君 津製鐵所内 (72)発明者 小松 久芳 君津市君津1番地 新日本製鐵株式会社君 津製鐵所内 (72)発明者 三宅 豪 君津市君津1番地 新日本製鐵株式会社君 津製鐵所内 (72)発明者 森本 康秀 富津市新富20−1 新日本製鐵株式会社技 術開発本部内 (72)発明者 西村 一実 姫路市広畑区富士町1番地 新日本製鐵株 式会社広畑製鐵所内 (72)発明者 本田 和彦 君津市君津1番地 新日本製鐵株式会社君 津製鐵所内 (72)発明者 高橋 靖雄 富津市新富20−1 新日本製鐵株式会社技 術開発本部内 Fターム(参考) 4K027 AA02 AA05 AA22 AB05 AB13 AB44 AC52 AC82 AC87 AE02 4K044 AA02 AB02 BA10 BA12 BA17 BA21 BB03 BC02 BC08 CA11 CA16 CA53 Continued on the front page (72) Inventor Akira Takahashi 1 Kimitsu, Kimitsu-shi Nippon Steel Corporation Kimitsu Works (72) Inventor Hisayoshi Komatsu 1 Kimitsu, Kimitsu-shi Nippon Steel Corporation Kimitsu Works (72) Inventor Go Miyake 1 Kimitsu City, Kimitsu City Nippon Steel Corporation Kimitsu Works (72) Inventor Yasuhide Morimoto 20-1 Shintomi, Futtsu City Nippon Steel Corporation Technology Development Division (72) Inventor Kazumi Nishimura 1 Fujimachi, Hirohata-ku, Himeji-shi Inside Hirohata Works, Nippon Steel Corporation (72) Inventor Kazuhiko Honda 1 Kimitsu, Kimitsu-shi Inside Kimitsu Works, Nippon Steel Corporation (72) Inventor Yasuo Takahashi 20-1 Shintomi, Futtsu-shi Nippon Steel Corporation Technology Development Division F-term (reference) 4K027 AA02 AA05 AA22 AB05 AB13 AB44 AC52 AC82 AC87 AE02 4K044 AA02 AB02 BA10 BA12 BA12 BA17 BA21 BB03 BC02 BC08 CA11 CA16 CA53
Claims (6)
%、Si:0.01〜2%を含み、残部Zn及び不可避
的不純物とからなるめっき層を有し、100μm2以上
の面積のSi系物質をめっき層の単位断面積当たり6×
103個以下含有することを特徴とするスポット溶接性
に優れた溶融亜鉛−アルミニウム合金めっき鋼板。1. Al: 3 to 20% by mass on the surface of a steel sheet.
%, Si: 0.01 to 2%, the balance having a plating layer composed of Zn and inevitable impurities, and a Si-based material having an area of 100 μm 2 or more per unit cross-sectional area of the plating layer being 6 ×
Molten zinc excellent in spot weldability characterized by containing 10 3 or less - aluminum alloy coated steel sheet.
中にさらに、Mg:0.1〜10%を含有することを特
徴とするスポット溶接性に優れた溶融亜鉛−アルミニウ
ム合金めっき鋼板。2. A hot-dip zinc-aluminum alloy coated steel sheet excellent in spot weldability, characterized in that the coating layer of the coated steel sheet according to claim 1 further contains Mg: 0.1 to 10%.
板のめっき層中にさらに、Ti、Cr、Ni、Snの1
種以上を質量%で0.01〜2%含有することを特徴と
するスポット溶接性に優れた溶融亜鉛−アルミニウム合
金めっき鋼板。3. The plating layer of the plated steel sheet according to claim 1, further comprising one of Ti, Cr, Ni, and Sn.
A hot-dip zinc-aluminum alloy-plated steel sheet having excellent spot weldability, characterized by containing 0.01% to 2% by mass of at least one kind.
のめっき鋼板のめっき層の上に無機酸化物皮膜を70m
g/m2〜2g/m2有することを特徴とするスポット溶
接性に優れた溶融亜鉛−アルミニウム合金めっき鋼板。4. An inorganic oxide film having a thickness of 70 m on a plating layer of the plated steel sheet according to any one of claims 1 to 3.
molten zinc excellent in spot weldability characterized by having g / m 2 ~2g / m 2 - aluminum alloy coated steel sheet.
のめっき鋼板のめっき層の上に有機樹脂皮膜を100m
g/m2〜2g/m2有することを特徴とするスポット溶
接性に優れた溶融亜鉛−アルミニウム合金めっき鋼板。5. An organic resin film having a thickness of 100 m on a plating layer of the plated steel sheet according to any one of claims 1 to 3.
molten zinc excellent in spot weldability characterized by having g / m 2 ~2g / m 2 - aluminum alloy coated steel sheet.
を製造するに際し、めっき浴温を400℃以上とするこ
とにより、めっき層中に100μm2以上の面積のSi
系物質をめっき層の単位断面積当たり6×103個以下
含有させることを特徴とする請求項1乃至請求項5のい
ずれかに記載のスポット溶接性に優れた溶融亜鉛−アル
ミニウム合金めっき鋼板の製造方法。6. When producing a hot-dip zinc-aluminum alloy-plated steel sheet, by setting the plating bath temperature to 400 ° C. or higher, the area of 100 μm 2 or more Si
The hot-dip zinc-aluminum alloy-coated steel sheet having excellent spot weldability according to any one of claims 1 to 5, wherein the coating material contains 6 x 10 3 or less per unit sectional area of the plating layer. Production method.
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Cited By (7)
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JP2004225157A (en) * | 2002-11-27 | 2004-08-12 | Nippon Steel Corp | Highly corrosion-resistant coated steel plate having excellent sharpness |
JP2007084844A (en) * | 2005-09-20 | 2007-04-05 | Nippon Steel Corp | Highly corrosion-resistant hot-dip plated steel sheet excellent in weldability, and its manufacturing method |
JP2007146199A (en) * | 2005-11-25 | 2007-06-14 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
JP2012007243A (en) * | 2011-09-27 | 2012-01-12 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
JP2016124029A (en) * | 2015-01-08 | 2016-07-11 | 新日鐵住金株式会社 | Superposition blank for hot stamping, method for producing superposition hot-stamp molded article, and superposition hot-stamp molded article |
EP3608442A4 (en) * | 2017-03-27 | 2020-09-09 | Nippon Steel Corporation | Al-based plated steel sheet |
CN116457483A (en) * | 2020-11-18 | 2023-07-18 | 日本制铁株式会社 | Plated steel material |
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Publication number | Priority date | Publication date | Assignee | Title |
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CN116457483A (en) * | 2020-11-18 | 2023-07-18 | 日本制铁株式会社 | Plated steel material |
CN116457483B (en) * | 2020-11-18 | 2024-04-19 | 日本制铁株式会社 | Plated steel material |
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