JP2020007586A - HOT-DIP Al-Zn BASED PLATED STEEL SHEET AND METHOD FOR MANUFACTURING THE SAME - Google Patents
HOT-DIP Al-Zn BASED PLATED STEEL SHEET AND METHOD FOR MANUFACTURING THE SAME Download PDFInfo
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Abstract
Description
本発明は、溶融Al−Zn系めっき鋼板及びその製造方法に関する。 The present invention relates to a hot-dip Al-Zn plated steel sheet and a method for producing the same.
耐食性に優れる溶融Al−Zn系めっき鋼板は、その優れた耐食性から、長期間屋外に曝される屋根や壁等の建材分野を中心に需要が伸びている。自動車分野においては、地球温暖化対策の一環として、車体を軽量化することによって燃費を向上させることにより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とが強く望まれている。 Due to its excellent corrosion resistance, demand for hot-dip Al-Zn-based plated steel sheets having excellent corrosion resistance is growing mainly in the field of construction materials such as roofs and walls exposed outdoors for a long time. In the automobile field, as a part of measures against global warming, it is required to reduce CO 2 emissions by improving fuel efficiency by reducing the weight of a vehicle body. For this reason, it is now strongly desired to reduce the weight by using a high-strength steel sheet and to reduce the gauge by improving the corrosion resistance of the steel sheet.
しかしながら、溶融Al−Zn系めっき鋼板を自動車分野、特に外板パネル等の車体に用いようとした場合、化成処理性が劣るという課題があった。 However, when using a hot-dip Al-Zn-based plated steel sheet in the automobile field, particularly in a vehicle body such as an outer panel, there has been a problem that the chemical conversion property is poor.
本発明は、上記課題に鑑みてなされたものであって、その目的は、化成処理性を向上可能な溶融Al−Zn系めっき鋼板及びその製造方法を提供することにある。 The present invention has been made in view of the above problems, and an object of the present invention is to provide a hot-dip Al-Zn-based plated steel sheet capable of improving chemical conversion treatment and a method for manufacturing the same.
本発明に係る溶融Al−Zn系めっき鋼板は、鋼板の表面に形成された、少なくともAl,Si,及びFeを含有する合金層と、前記合金層の表面に形成された、少なくともAl,Zn,Si,及びCuを含有するめっき層と、を有し、前記めっき層のAl含有率が原子%濃度で40%以上90%以下の範囲内にあり、前記めっき層のSi含有率が原子%濃度で0.2%以上3%以下の範囲内にあることを特徴とする。 The hot-dip Al—Zn-based plated steel sheet according to the present invention includes an alloy layer containing at least Al, Si, and Fe formed on the surface of the steel sheet, and at least Al, Zn, and Fe formed on the surface of the alloy layer. A plating layer containing Si and Cu, wherein the Al content of the plating layer is in the range of 40% to 90% in atomic% concentration, and the Si content of the plating layer is in atomic% concentration. In the range of 0.2% or more and 3% or less.
本発明に係る溶融Al−Zn系めっき鋼板は、上記発明において、前記めっき層のCu含有率が原子%濃度で0.05%以上3%以下の範囲内にあることを特徴とする。 The hot-dip Al-Zn-based plated steel sheet according to the present invention is characterized in that, in the above invention, the Cu content of the plating layer is in the range of 0.05% to 3% in atomic% concentration.
本発明に係る溶融Al−Zn系めっき鋼板は、上記発明において、前記めっき層がMg,Ca,Ti,Mnの中から選ばれる1種以上の元素をそれぞれの原子%濃度の合計で10%以下の範囲内含有することを特徴とする。 The hot-dip Al—Zn-based plated steel sheet according to the present invention, in the above invention, wherein the plating layer contains at least one element selected from Mg, Ca, Ti, and Mn in a total of 10% or less in atomic% concentration. Is contained within the range.
本発明に係る溶融Al−Zn系めっき鋼板は、上記発明において、X線回折で得られるAl相[111]の回折強度{I(Al)}に対するAl2Cu相[222]の回折強度{I(Al2Cu)}のメインピーク強度の比率Y=I(Al2Cu)/I(Al)が0.02以下であることを特徴とする。 The hot-dip Al—Zn-based plated steel sheet according to the present invention according to the above invention, wherein the diffraction intensity ΔI of the Al 2 Cu phase [222] with respect to the diffraction intensity {I (Al)} of the Al phase [111] obtained by X-ray diffraction. (Al 2 Cu)} The main peak intensity ratio Y = I (Al 2 Cu) / I (Al) is 0.02 or less.
本発明に係る溶融Al−Zn系めっき鋼板の製造方法は、本発明に係る溶融Al−Zn系めっき鋼板の製造方法であって、いずれも原子%濃度でAl:40%以上90%以下、Si:0.2%以上3%以下、Fe:2%以下、Cu:0.05%以上3%以下、Mg,Ca,Ti,Mnの中から選ばれる1種以上の元素を合計で10%以下の範囲内含有し、残部がZn及び不可避的不純物からなり、温度が580℃以上620℃以下の範囲内にある溶融金属浴に前記鋼板を浸漬した後、570℃から500℃までの平均冷却速度を10℃/s以上として急速冷却を施すステップを含むことを特徴とする。 The method for producing a hot-dip Al-Zn plated steel sheet according to the present invention is a method for producing a hot-dip Al-Zn plated steel sheet according to the present invention, and each of them has an atomic percent concentration of Al: 40% or more and 90% or less; : 0.2% or more and 3% or less, Fe: 2% or less, Cu: 0.05% or more and 3% or less, and 10% or less in total of one or more elements selected from Mg, Ca, Ti, and Mn , The balance consisting of Zn and unavoidable impurities, and immersing the steel sheet in a molten metal bath having a temperature in the range of 580 ° C to 620 ° C, and then the average cooling rate from 570 ° C to 500 ° C. At a rate of 10 ° C./s or more to perform rapid cooling.
本発明によれば、化成処理性を向上可能な溶融Al−Zn系めっき鋼板及びその製造方法を提供することができる。 ADVANTAGE OF THE INVENTION According to this invention, the hot-dip Al-Zn-type plated steel sheet which can improve chemical conversion treatment property and its manufacturing method can be provided.
以下、本発明に係る溶融Al−Zn系めっき鋼板及びその製造方法について説明する。なお、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「原子%濃度(at%)」であり、以下、特に断らない限り単に「%」で示す。 Hereinafter, a hot-dip Al-Zn-based plated steel sheet and a method for manufacturing the same according to the present invention will be 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 “atomic% concentration (at%)”, and hereinafter, simply indicated by “%” unless otherwise specified. .
〔溶融Al−Zn系めっき鋼板の構成〕
まず、本発明に係る溶融Al−Zn系めっき鋼板の構成について説明する。
[Configuration of hot-dip Al-Zn plated steel sheet]
First, the configuration of the hot-dip Al-Zn-based plated steel sheet according to the present invention will be described.
本発明に係る溶融Al−Zn系めっき鋼板は、鋼板と、鋼板の表面に形成された、少なくともAl,Si,及びFeを含有する合金層と、合金層の表面に形成された、少なくともAl,Zn,Si,及びCuを含有するめっき層と、を有している。めっき層は、初晶Alを主体としたデンドライト部分とZnリッチなインターデンドライト部分とからなる、2相構造を有している。 The hot-dip Al-Zn-based coated steel sheet according to the present invention includes a steel sheet, an alloy layer containing at least Al, Si, and Fe formed on the surface of the steel sheet, and at least Al, Zn formed on the surface of the alloy layer. And a plating layer containing Zn, Si, and Cu. The plating layer has a two-phase structure including a dendrite portion mainly composed of primary Al and a Zn-rich interdendrite portion.
めっき層のAl含有率は40%以上90%以下の範囲内にある。Al含有率が40%未満である場合、めっき層においてAlリッチ相とZnリッチ相の体積比が逆転し、耐食性が極端に低下する。一方、Al含有率が90%超である場合には、Znリッチ相が消失し、めっき層がZnを固溶したAl単相となり、この場合も耐食性が著しく低下する。 The Al content of the plating layer is in the range of 40% or more and 90% or less. When the Al content is less than 40%, the volume ratio of the Al-rich phase and the Zn-rich phase in the plating layer is reversed, and the corrosion resistance is extremely reduced. On the other hand, when the Al content is more than 90%, the Zn-rich phase disappears, and the plating layer becomes an Al single phase in which Zn is dissolved, and also in this case, the corrosion resistance is significantly reduced.
めっき層のSi含有率は0.2%以上3%以下の範囲内にある。Si含有率が0.2%未満である場合、Fe−Al合金層の成長を抑制できない。一方、Si含有率が3%超である場合には、単相Siがめっき層中に析出し、局部腐食の起点となる場合がある。 The Si content of the plating layer is in the range of 0.2% or more and 3% or less. If the Si content is less than 0.2%, the growth of the Fe-Al alloy layer cannot be suppressed. On the other hand, when the Si content is more than 3%, single-phase Si may precipitate in the plating layer and become a starting point of local corrosion.
めっき層のCu含有率は0.05%以上3%以下の範囲内にある。Cuをめっき層に含有することにより、化成処理時にめっき表面に電位勾配が生じ、局所的にpHが上昇し化成結晶の生成を促進できる。Cu含有率が0.05%未満である場合、十分な化成処理性改善効果が得られない。一方、Cu含有率が3%超である場合には、Al2Cu相の析出量が急激に増加し、耐食性が低下する。 The Cu content of the plating layer is in the range of 0.05% or more and 3% or less. By containing Cu in the plating layer, a potential gradient is generated on the plating surface during the chemical conversion treatment, and the pH is locally increased to promote the formation of chemical conversion crystals. If the Cu content is less than 0.05%, a sufficient effect of improving the chemical conversion treatment property cannot be obtained. On the other hand, when the Cu content is more than 3%, the precipitation amount of the Al 2 Cu phase sharply increases, and the corrosion resistance decreases.
めっき層はMg,Ca,Ti,Mnの中から選ばれる1種以上の元素を合計で10%以下の範囲内含有することもできる。これらの元素を含有することで、めっき層の組織が微細化し、化成処理性の改善とより優れた耐食性とを高度に両立できる。 The plating layer may contain one or more elements selected from Mg, Ca, Ti, and Mn in a range of 10% or less in total. By containing these elements, the structure of the plating layer becomes finer, and it is possible to achieve a high degree of compatibility between improvement in chemical conversion treatment and more excellent corrosion resistance.
X線回折で得られるAl相[111]の回折強度{I(Al)}に対するAl2Cu相[222]の回折強度{I(Al2Cu)}のメインピーク強度の比率Y=I(Al2Cu)/I(Al)は0.02以下である。比率Yが0.02超であることは、Al2Cu相がめっき層の表層に過剰に析出していることを示し、化成処理性に優れた合金組成であっても耐食性に劣った皮膜となる可能性がある。比率Yと製造パラメータの相関は明らかでないが、浴中Cu量の増大及びめっき後の冷却速度の低下により増大する傾向にある。 Ratio of main peak intensity of diffraction intensity {I (Al 2 Cu)} of Al 2 Cu phase [222] to diffraction intensity {I (Al)} of Al phase [111] obtained by X-ray diffraction Y = I (Al) 2 Cu) / I (Al) is 0.02 or less. When the ratio Y is more than 0.02, it indicates that the Al 2 Cu phase is excessively precipitated on the surface layer of the plating layer, and a film having poor corrosion resistance even with an alloy composition having excellent chemical conversion property. Could be. Although the correlation between the ratio Y and the production parameter is not clear, it tends to increase due to an increase in the amount of Cu in the bath and a decrease in the cooling rate after plating.
〔溶融Al−Zn系めっき鋼板の製造方法〕
本発明に係る溶融Al−Zn系めっき鋼板の製造方法は、本発明に係る溶融Al−Zn系めっき鋼板を製造する際、Al:40%以上90%以下、Si:0.2%以上3%以下、Fe:2%以下、Cu:0.05%以上3%以下、Mg,Ca,Ti,Mnの中から選ばれる1種以上の元素を合計で10%以下の範囲内含有し、残部がZn及び不可避的不純物からなり、温度が580℃以上620℃以下の範囲内にある溶融金属浴に鋼板を浸漬した後、570℃から500℃までの平均冷却速度を10℃/s以上として急速冷却を施すステップを含む。
[Production method of hot-dip Al-Zn plated steel sheet]
The method for producing a hot-dip Al-Zn-based coated steel sheet according to the present invention is characterized in that, when manufacturing the hot-dip Al-Zn-based coated steel sheet according to the present invention, Al: 40% or more and 90% or less, Si: 0.2% or more and 3% or less. Hereinafter, Fe: 2% or less, Cu: 0.05% or more and 3% or less, one or more elements selected from Mg, Ca, Ti, and Mn are contained in a range of 10% or less in total, and the balance is After immersing the steel sheet in a molten metal bath composed of Zn and unavoidable impurities and having a temperature in the range of 580 ° C or more and 620 ° C or less, rapid cooling at an average cooling rate of 570 ° C to 500 ° C of 10 ° C / s or more is performed. Performing the following.
次に、本発明の実施例について説明する。 Next, examples of the present invention will be described.
(サンプル1〜40)
サンプルとなる全ての溶融Al−Zn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、溶融めっき設備において、めっき浴の浴温を600℃、浸入温度を620℃、ラインスピード60mpm、浸漬時間2秒で、めっき浴の組成を種々の条件に変化させ、各サンプルの溶融Al−Zn系めっき鋼板を製造した。なお、めっき浴の組成は、サンプルの製造に用いためっき浴から約2gを採取し、化学分析によって確認した。各サンプルのめっき浴の組成を以下の表1に示す。また、めっき浴浸漬後の窒素ガスによる冷却の570℃から500℃までの冷却速度を以下の表1に示す。さらに、界面合金層及びめっき層の組成としては、各サンプルの溶融Al−Zn系めっき鋼板から任意の3断面を剪断加工により切り出し、カーボン樹脂に埋め込んだ上でSEM−EDX観察を行い、界面合金層及びめっき層のうち任意の5点でEDXにより測定した半定量分析値の平均値を用いた。各サンプルの界面合金層及びめっき層の組成を以下の表1に示す。
(Samples 1 to 40)
For all the hot-dip Al-Zn-based coated steel sheets to be used as samples, a cold-rolled steel sheet with a thickness of 0.8 mm manufactured by a conventional method is used as a base steel sheet. At 620 ° C., a line speed of 60 mpm, and an immersion time of 2 seconds, the composition of the plating bath was changed to various conditions, and a hot-dip Al—Zn-based plated steel sheet of each sample was manufactured. The composition of the plating bath was confirmed by collecting about 2 g of the plating bath used for producing the sample and performing chemical analysis. The composition of the plating bath for each sample is shown in Table 1 below. Table 1 below shows the cooling rate from 570 ° C. to 500 ° C. of cooling by nitrogen gas after immersion in the plating bath. Furthermore, as for the composition of the interface alloy layer and the plating layer, three arbitrary cross sections were cut out from the molten Al-Zn-based plated steel sheet of each sample by shearing, embedded in carbon resin, and observed by SEM-EDX. The average value of the semi-quantitative analysis values measured by EDX at any five points of the layer and the plating layer was used. Table 1 shows the compositions of the interface alloy layer and the plating layer of each sample.
各サンプルの溶融Al−Zn系めっき鋼板の比率Y、化成処理性、裸耐食性、及び塗装後耐食性を以下に示す方法により評価した。 The ratio Y of the hot-dip Al-Zn-based plated steel sheet of each sample, the chemical conversion property, the bare corrosion resistance, and the corrosion resistance after coating were evaluated by the following methods.
1.比率Y
Al相[111]の回折強度{I(Al)}に対するAl2Cu相[222]の回折強度{I(Al2Cu)}のメインピーク強度の比率Y=I(Al2Cu)/I(Al)は、Cu−Kα線を使用したX線回折装置により回折図形を測定し判定した。
1. Ratio Y
The ratio of the diffraction intensity {I (Al)} of the Al phase [111] to the main peak intensity of the diffraction intensity {I (Al 2 Cu)} of the Al 2 Cu phase [222] Y = I (Al 2 Cu) / I ( Al) was determined by measuring a diffraction pattern with an X-ray diffractometer using Cu-Kα rays.
2.化成処理性
市販の化成処理薬剤(日本パーカライジング株式会社製パルボンドSX−35)を用いて、浴温:35℃、フリーフッ素濃度:200質量ppm、処理時間:120秒の条件で鋼板の化成処理を行った後、めっき鋼板の表面を走査型電子顕微鏡にて1000倍で10視野観察した。結晶の形態については、面積率98%以上の均一な化成結晶が10視野全てにおいて生成しているものを優(◎)、面積率98%未満の視野が1視野認められるものを良(○)、面積率98%未満の視野が2視野認められるものを可(△)とし、面積率98%未満の視野が3視野以上認められるものを不可(×)として評価した。なお、ここでいう隙間とは、均一な化成結晶が生成していない箇所のことを指し、反射電子像を2値化することにより空隙の面積率を算出した。また、結晶の付着量については、化成処理試験後の試料3点を20g/Lの重クロム酸アンモニウム水溶液に15分間浸漬し、前後の重量差から試験片面積当たりの値として算出した。結晶の付着量は、3点すべてにおいて2.0g/m2以上のものを優(◎)、1.8g/m2以上2.0g/m2未満のものを良(○)、1.5g/m2以上1.8g/m2未満のものを可(△)、1.5g/m2未満のものが1点でも認められるものを不可(×)として評価した。
2. Chemical conversion treatment Using a commercially available chemical conversion chemical (PALBOND SX-35 manufactured by Nippon Parkerizing Co., Ltd.), the steel plate was subjected to chemical conversion under the conditions of bath temperature: 35 ° C, free fluorine concentration: 200 mass ppm, and treatment time: 120 seconds. After performing, the surface of the plated steel sheet was observed with a scanning electron microscope at 1000 magnifications for 10 fields of view. Regarding the morphology of the crystals, excellent (◎) means that a uniform chemical conversion crystal having an area ratio of 98% or more is generated in all 10 visual fields, and good (○) means that one visual field having an area ratio of less than 98% is recognized. The case where two visual fields having an area ratio of less than 98% were recognized was evaluated as acceptable (△), and the case where three or more visual fields having an area ratio of less than 98% were observed was evaluated as unacceptable (x). Here, the gap refers to a place where a uniform chemical conversion crystal is not generated, and the area ratio of the gap is calculated by binarizing the reflected electron image. Regarding the amount of attached crystals, three samples after the chemical conversion treatment test were immersed in a 20 g / L aqueous solution of ammonium bichromate for 15 minutes, and calculated from the difference in weight before and after as a value per test piece area. At all three points, the adhesion amount of the crystals was 2.0 g / m 2 or more excellent (に お い て), 1.8 g / m 2 or more and less than 2.0 g / m 2 good (○), 1.5 g / G / m 2 or more and less than 1.8 g / m 2 were evaluated as acceptable (△), and those with less than 1.5 g / m 2 even at one point were evaluated as unacceptable (x).
3.裸耐食性
各サンプルの溶融Al−Zn系めっき鋼板について、JIS Z2371−2000に準拠した塩水噴霧試験を行った。各サンプルの赤錆が発生するまでの時間を測定し、以下の基準により裸耐食性を評価した。評価結果を以下の表1に示す。
3. Bare corrosion resistance A salt spray test based on JIS Z2371-2000 was performed on the hot-dip Al-Zn-based plated steel sheet of each sample. The time until red rust of each sample was measured, and the bare corrosion resistance was evaluated according to the following criteria. The evaluation results are shown in Table 1 below.
◎:赤錆発生時間≧600時間
○:300時間≦赤錆発生時間<600時間
△:150時間≦赤錆発生時間<300時間
×:赤錆発生時間<150時間
:: Red rust occurrence time ≧ 600 hours ○: 300 hours ≦ Red rust occurrence time <600 hours Δ: 150 hours ≦ Red rust occurrence time <300 hours ×: Red rust occurrence time <150 hours
4.塗装後耐食性
各サンプルの溶融Al−Zn系めっき鋼板について、それぞれ70mm×80mm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、電着塗装を施した。ここで、リン酸亜鉛処理及び電着塗装は以下の条件で行った。
4. Corrosion resistance after painting About the hot-dip Al-Zn-based plated steel sheet of each sample, after shearing to the size of 70 mm x 80 mm, and performing zinc phosphate treatment as a chemical conversion treatment in the same manner as coating treatment for automobile outer panels, electrodeposition coating gave. Here, the zinc phosphate treatment and the electrodeposition coating were performed under the following conditions.
リン酸亜鉛処理:市販の化成処理薬剤(日本パーカライジング株式会社製パルボンドSX−35)を用いて、浴温:35℃、フリーフッ素濃度:200質量ppm、処理時間:120秒の条件で鋼板の化成処理を行った。 Zinc phosphate treatment: Using a commercially available chemical conversion treatment agent (PALBOND SX-35 manufactured by Nippon Parkerizing Co., Ltd.), forming a steel sheet under the conditions of bath temperature: 35 ° C., free fluorine concentration: 200 mass ppm, and treatment time: 120 seconds. Processing was performed.
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。 Electrodeposition coating: Electrodeposition coating was performed using Kansai Paint's electrodeposition coating: GT-100 so that the film thickness became 15 μm.
化成処理及び電着塗装後、評価面の端部7.5mm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60°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て用いた。 After the chemical conversion treatment and the electrodeposition coating, the edge of the evaluation surface 7.5 mm and the non-evaluation surface (back surface) are sealed with a tape, and the depth of reaching the base steel of the plated steel sheet with a cutter knife at the center of the evaluation surface. A cross-cut flaw having a length of 60 mm and a central angle of 60 ° was used as a sample for evaluation of corrosion resistance after painting.
上記評価用サンプルを用いて、SAE J2334に規定された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状態からスタートし、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、塗装後耐食性を以下の基準で評価した。評価結果を以下の表1に示す。 Using the sample for evaluation, a corrosion acceleration test was performed in a cycle specified in SAE J2334. After the corrosion promotion test was started from the wet state and was performed up to 60 cycles, the coating swelling width of the portion where the coating swelling from the scratch was the largest (maximum coating swelling width: one side with the scratch at the center) The maximum coating blister width was measured, and the corrosion resistance after coating was evaluated according to the following criteria. The evaluation results are shown in Table 1 below.
◎:最大塗膜膨れ幅≦2.5mm
○:2.5mm<最大塗膜膨れ幅≦4.0mm
△:4.0mm<最大塗膜膨れ幅≦5.0mm
×:最大塗膜膨れ幅>5.0mm
◎: maximum coating blister width ≦ 2.5 mm
:: 2.5 mm <maximum coating blister width ≦ 4.0 mm
Δ: 4.0 mm <maximum swollen film width ≦ 5.0 mm
×: Maximum coating swollen width> 5.0 mm
以下の表1に示すように、比較例では化成処理性が不足しているか、あるいはAl2Cu相が過剰となり、いずれも塗装後耐食性に不足があった。これに対して、本発明例は化成処理性及び塗装後耐食性共に優れていた。これにより、本発明によれば、溶融Al−Zn系めっき鋼板の化成処理性を向上させることにより塗装後耐食性を改善可能であることが確認された。 As shown in Table 1 below, in the comparative example, the chemical conversion treatment property was insufficient, or the Al 2 Cu phase was excessive, and all had insufficient corrosion resistance after painting. On the other hand, the examples of the present invention were excellent in both chemical conversion property and corrosion resistance after painting. Thus, according to the present invention, it was confirmed that the post-paint corrosion resistance can be improved by improving the chemical conversion property of the hot-dip Al-Zn-based plated steel sheet.
めっき層のCu含有率は0.05%以上3%以下の範囲内にあることが好ましい。Cuをめっき層に含有することにより、化成処理時にめっき表面に電位勾配が生じ、局所的にpHが上昇し化成結晶の生成を促進できる。Cu含有率が0.05%未満である場合、十分な化成処理性改善効果が得られない。一方、Cu含有率が3%超である場合には、Al2Cu相の析出量が急激に増加し、耐食性が低下する。 The Cu content of the plating layer is preferably in the range of 0.05% or more and 3% or less. By containing Cu in the plating layer, a potential gradient is generated on the plating surface during the chemical conversion treatment, and the pH is locally increased to promote the formation of chemical conversion crystals. If the Cu content is less than 0.05%, a sufficient effect of improving the chemical conversion treatment property cannot be obtained. On the other hand, when the Cu content is more than 3%, the precipitation amount of the Al 2 Cu phase sharply increases, and the corrosion resistance decreases.
X線回折で得られるAl相[111]の回折強度{I(Al)}に対するAl2Cu相[222]の回折強度{I(Al2Cu)}のメインピーク強度の比率Y=I(Al2Cu)/I(Al)は0.02以下であることが好ましい。比率Yが0.02超であることは、Al2Cu相がめっき層の表層に過剰に析出していることを示し、化成処理性に優れた合金組成であっても耐食性に劣った皮膜となる可能性がある。比率Yと製造パラメータの相関は明らかでないが、浴中Cu量の増大及びめっき後の冷却速度の低下により増大する傾向にある。 Ratio of main peak intensity of diffraction intensity {I (Al 2 Cu)} of Al 2 Cu phase [222] to diffraction intensity {I (Al)} of Al phase [111] obtained by X-ray diffraction Y = I (Al) 2 Cu) / I (Al) is preferably 0.02 or less. When the ratio Y is more than 0.02, it indicates that the Al 2 Cu phase is excessively precipitated on the surface layer of the plating layer, and a film having poor corrosion resistance even with an alloy composition having excellent chemical conversion property. Could be. Although the correlation between the ratio Y and the production parameter is not clear, it tends to increase due to an increase in the amount of Cu in the bath and a decrease in the cooling rate after plating.
〔溶融Al−Zn系めっき鋼板の製造方法〕
本発明に係る溶融Al−Zn系めっき鋼板の製造方法は、本発明に係る溶融Al−Zn系めっき鋼板を製造する際、Al:40%以上90%以下、Si:0.2%以上3%以下、Fe:2%以下、Cu:0.05%以上3%以下、Mg,Ca,Ti,Mnの中から選ばれる1種以上の元素を合計で10%以下の範囲内含有し、残部がZn及び不可避的不純物からなり、温度が580℃以上620℃以下の範囲内にある溶融金属浴に鋼板を浸漬した後、鋼板を取り出し、570℃から500℃までの平均冷却速度を10℃/s以上として急速冷却を施すステップを含む。
[Production method of hot-dip Al-Zn plated steel sheet]
The method for producing a hot-dip Al-Zn-based coated steel sheet according to the present invention is characterized in that, when manufacturing the hot-dip Al-Zn-based coated steel sheet according to the present invention, Al: 40% or more and 90% or less, Si: 0.2% or more and 3% or less. Hereinafter, Fe: 2% or less, Cu: 0.05% or more and 3% or less, one or more elements selected from Mg, Ca, Ti, and Mn are contained in a range of 10% or less in total, and the balance is After immersing the steel sheet in a molten metal bath consisting of Zn and unavoidable impurities and having a temperature in the range of 580 ° C or more and 620 ° C or less, the steel sheet is taken out, and the average cooling rate from 570 ° C to 500 ° C is set at 10 ° C / s. The above includes the step of performing rapid cooling.
(サンプル1〜40)
サンプルとなる全ての溶融Al−Zn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、溶融めっき設備において、めっき浴の浴温を600℃、鋼板の浸入温度を620℃、ラインスピード60mpm、浸漬時間2秒で、めっき浴の組成を種々の条件に変化させ、各サンプルの溶融Al−Zn系めっき鋼板を製造した。なお、めっき浴の組成は、サンプルの製造に用いためっき浴から約2gを採取し、化学分析によって確認した。各サンプルのめっき浴の組成を以下の表1に示す。また、めっき浴浸漬後の窒素ガスによる冷却の570℃から500℃までの冷却速度を以下の表1に示す。さらに、界面合金層及びめっき層の組成としては、各サンプルの溶融Al−Zn系めっき鋼板から任意の3断面を剪断加工により切り出し、カーボン樹脂に埋め込んだ上でSEM−EDX観察を行い、界面合金層及びめっき層のうち任意の5点でEDXにより測定した半定量分析値の平均値を用いた。各サンプルの界面合金層及びめっき層の組成を以下の表1に示す。
(Samples 1 to 40)
For all hot-dip Al-Zn coated steel sheets to be used as samples, a cold-rolled steel sheet with a thickness of 0.8 mm manufactured by a conventional method is used as a base steel sheet. The infiltration temperature was 620 ° C., the line speed was 60 mpm, and the immersion time was 2 seconds. The composition of the plating bath was changed to various conditions, and hot-dip Al—Zn-based plated steel sheets of each sample were manufactured. The composition of the plating bath was confirmed by collecting about 2 g of the plating bath used for producing the sample and performing chemical analysis. The composition of the plating bath for each sample is shown in Table 1 below. Table 1 below shows the cooling rate from 570 ° C. to 500 ° C. of cooling by nitrogen gas after immersion in the plating bath. Furthermore, as for the composition of the interface alloy layer and the plating layer, three arbitrary sections were cut out from the molten Al-Zn-based plated steel sheet of each sample by shearing, embedded in a carbon resin, and observed by SEM-EDX. The average value of the semi-quantitative analysis values measured by EDX at any five points of the layer and the plating layer was used. Table 1 shows the compositions of the interface alloy layer and the plating layer of each sample.
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Citations (4)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPH0364438A (en) * | 1989-07-31 | 1991-03-19 | Kawasaki Steel Corp | Manufacture of hot dip aluminized chromium-containing steel sheet |
JP2004143506A (en) * | 2002-10-23 | 2004-05-20 | Nippon Steel Corp | Hot dip plated steel sheet having excellent appearance quality, and production method for the hot dip plated steel sheet |
JP2004232029A (en) * | 2003-01-30 | 2004-08-19 | Jfe Steel Kk | COATED HOT DIP Al-Zn BASED ALLOY PLATED STEEL SHEET HAVING EXCELLENT SURFACE APPEARANCE, AND PRODUCTION METHOD THEREFOR |
JP2012126994A (en) * | 2010-11-26 | 2012-07-05 | Jfe Steel Corp | Al-Zn-BASED HOT-DIP PLATED STEEL SHEET |
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---|---|---|---|---|
JPH0364438A (en) * | 1989-07-31 | 1991-03-19 | Kawasaki Steel Corp | Manufacture of hot dip aluminized chromium-containing steel sheet |
JP2004143506A (en) * | 2002-10-23 | 2004-05-20 | Nippon Steel Corp | Hot dip plated steel sheet having excellent appearance quality, and production method for the hot dip plated steel sheet |
JP2004232029A (en) * | 2003-01-30 | 2004-08-19 | Jfe Steel Kk | COATED HOT DIP Al-Zn BASED ALLOY PLATED STEEL SHEET HAVING EXCELLENT SURFACE APPEARANCE, AND PRODUCTION METHOD THEREFOR |
JP2012126994A (en) * | 2010-11-26 | 2012-07-05 | Jfe Steel Corp | Al-Zn-BASED HOT-DIP PLATED STEEL SHEET |
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