JPH0551715A - Hot-dip zinc-aluminum alloy coated article excellent in fatigue characteristic - Google Patents
Hot-dip zinc-aluminum alloy coated article excellent in fatigue characteristicInfo
- Publication number
- JPH0551715A JPH0551715A JP3236824A JP23682491A JPH0551715A JP H0551715 A JPH0551715 A JP H0551715A JP 3236824 A JP3236824 A JP 3236824A JP 23682491 A JP23682491 A JP 23682491A JP H0551715 A JPH0551715 A JP H0551715A
- Authority
- JP
- Japan
- Prior art keywords
- plating
- aluminum alloy
- hot
- zinc
- dip zinc
- 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.)
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Abstract
Description
【０００１】[0001]
【産業上の利用分野】本発明は、溶融亜鉛アルミニウム
合金めっきにおける高耐食性及び美麗な外観を保持しな
がら疲労特性を著しく改善した被覆物に関する。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a coating which has a significantly improved fatigue property while maintaining high corrosion resistance and a beautiful appearance in hot dip aluminum alloy plating.
【０００２】[0002]
【従来の技術およびその問題点】溶融亜鉛アルミニウム
合金めっきはその簡便な手段により容易に高耐食性を備
えた被覆物を得ることができることから鋼材の防錆手段
として広く実施されている。さらに、例えば特公昭６３
−５０４１９号、特公昭６３−５０４２１号では、めっ
き被覆物の表面外観をより向上させるために、Ｚｎ−Ａ
ｌ合金に微量のナトリウムを含有させている。このよう
な従来の溶融亜鉛アルミニウム合金めっき被覆物によれ
ば、高耐食性と共に美麗な表面外観を有するため、通常
の使用環境においては、何ら問題は生じない。2. Description of the Related Art Hot-dip aluminum alloy plating is widely used as a rust preventive means for steel materials because a coating having high corrosion resistance can be easily obtained by a simple means. Further, for example, Japanese Patent Publication Sho 63
No. 50419 and Japanese Patent Publication No. 63-50421, in order to further improve the surface appearance of the plated coating, Zn-A
1 alloy contains a small amount of sodium. According to such a conventional hot-dip zinc aluminum alloy plated coating, it has high corrosion resistance and a beautiful surface appearance, so that no problem occurs in a normal use environment.
【０００３】しかしながら、溶融亜鉛めっき鋼材あるい
は溶融亜鉛アルミ合金めっき鋼材が、めっきを施してい
ない鋼材（以下、素材と記す）に比べて、疲労特性が場
合によっては２０〜３０％程度低下することが指摘され
ている（例えば、Scandinavian Journal of Metallurgy
18 166-175頁、1989、CAMP-ISIJ Vol.2 1680(1989)）。
この従来の被覆物における疲労特性の低下は、繰返し応
力が付加されるような使用環境、特に電線、ケーブル等
の長尺材では極めて重要な要素となる。However, the hot-dip galvanized steel material or the hot-dip galvanized aluminum alloy-plated steel material may have a fatigue property lower by about 20 to 30% depending on the case, as compared with the unplated steel material (hereinafter referred to as material). It has been pointed out (eg Scandinavian Journal of Metallurgy
18 166-175, 1989, CAMP-ISIJ Vol.2 1680 (1989)).
The deterioration of the fatigue properties of the conventional coating material is an extremely important factor in a use environment where repeated stress is applied, particularly in long materials such as electric wires and cables.
【０００４】これら疲労特性低下の原因としてめっきに
関係する要因として、 めっき層中に存在するＦｅ−Ｚｎ、Ｆｅ−Ａｌあるい
はＦｅ−Ａｌ−Ｚｎ系の硬くて脆い合金層（金属間化合
物）の発達、 合金層中に存在するマイクロクラック、ボイドの存
在、 めっき層の引張残留応力の存在、 めっき層表面の凹凸、マイクロクラックの存在、 めっき前処理時の水素吸蔵、 等の可能性が挙げられる。これらの要因は溶融めっきの
前処理、めっき浴組成、温度、浸漬時間等のめっき条件
とめっき後のワイピング、冷却条件によって複合的に生
じる現象であり、真の原因解明、対策の実施は難しい場
合も多い。As a factor related to the plating as a cause of the deterioration of the fatigue characteristics, the development of a hard and brittle alloy layer (intermetallic compound) of Fe-Zn, Fe-Al or Fe-Al-Zn system present in the plating layer. , Micro cracks existing in the alloy layer, voids, tensile residual stress in the plating layer, unevenness of the plating layer surface, micro cracks, hydrogen absorption during plating pretreatment, etc. are possible. These factors are phenomena that occur in combination depending on the plating conditions such as hot dipping pretreatment, plating bath composition, temperature, dipping time, and wiping and cooling conditions after plating.If it is difficult to elucidate the true cause and implement countermeasures There are also many.
【０００５】従来、疲労特性の改善方法としては、特開
平２−２５９０５４号のように、めっき後の冷却速度を
４〜１５℃／秒の一定範囲にコントロールする方法、あ
るいは特開平２−２９０９８１号のように、合金層厚さ
を２μｍ以下とする方法等が提案されている。Conventionally, as a method for improving fatigue characteristics, a method of controlling the cooling rate after plating within a fixed range of 4 to 15 ° C./second, as in JP-A-2-2599054, or JP-A-2-290981. As described above, a method of making the alloy layer thickness 2 μm or less has been proposed.
【０００６】しかしながら、特開平２−２５９０５４号
記載の方法は、合金層が厚い場合等、他の低下要因があ
る場合には、改善効果が十分でなく、現実にはめっき表
面にマイクロクラックが生じていなくてもめっき層内部
を起点として起こる疲労亀裂も多く観察されている。ま
た、特開平２−２９０９８１号記載の方法は、疲労特性
低下の主要な要因である合金層の厚さを薄くするという
意味ではかなり効果的な方法ではある。しかし、合金層
を２μｍ以下としても表面粗さの大きなめっき材では表
面を起点とする疲労亀裂に対しては効果が薄い。さら
に、合金層厚さを薄くし且つ全体めっき厚さのを維持す
るためには、引上速度を上昇させなければならず、めっ
き厚さの均一性維持、振動、偏肉防止のための操業技術
が難しくなる。また引上速度を変えずに合金層を薄くし
た場合には、全体めっき厚さが減少し、めっき厚さに依
存すると言われている耐食性が低下することとなる。こ
のように、各単独の要因のみのコントロールでは疲労特
性改善には不十分であり、より効果的で、しかも操業が
容易な改善方法が求められている。However, the method described in Japanese Patent Application Laid-Open No. 2-259054 is not sufficient in improving effect when there are other factors for lowering the thickness of the alloy layer or the like, and in reality, microcracks are generated on the plating surface. Even if not, many fatigue cracks originating from inside the plating layer are also observed. Further, the method described in JP-A-2-290981 is a very effective method in the sense that the thickness of the alloy layer, which is a main cause of deterioration of fatigue characteristics, is reduced. However, even if the alloy layer is 2 μm or less, a plated material having a large surface roughness is less effective against fatigue cracks starting from the surface. Further, in order to reduce the alloy layer thickness and maintain the overall plating thickness, the pulling speed must be increased, and the operation for maintaining the plating thickness uniformity, vibration, and uneven thickness prevention. Technology becomes difficult. Further, when the alloy layer is thinned without changing the pulling rate, the overall plating thickness is reduced and the corrosion resistance which is said to depend on the plating thickness is reduced. As described above, control of each individual factor is not sufficient to improve fatigue properties, and there is a need for a more effective and easy-to-operate improvement method.
【０００７】本発明は、上記のような現状に鑑み、高耐
食性及び美麗な外観を有する、微量のナトリウムを含有
した溶融亜鉛アルミニウム合金めっき被覆物に着目し、
その利点である高耐食性及び外観をそのまま保持しつ
つ、その疲労特性を大幅に改善し得る溶融亜鉛アルミニ
ウム合金めっき被覆物を提供することを目的とするもの
である。In view of the above situation, the present invention focuses on a hot-dip zinc aluminum alloy plated coating containing a trace amount of sodium, which has high corrosion resistance and a beautiful appearance,
It is an object of the present invention to provide a hot-dip zinc aluminum alloy plated coating capable of significantly improving its fatigue characteristics while maintaining its advantages of high corrosion resistance and appearance.
【０００８】[0008]
【問題点を解決するための手段】本発明では、アルミニ
ウム０．１〜３０重量％、ナトリウム０．００５〜０．
１０重量％を含有し、残部が不純物を別にして亜鉛から
なる溶融亜鉛アルミニウム合金めっきにおいて、Ｚｎ−
Ａｌ層と下地鋼材の界面に生成する合金層層を３０μｍ
未満とし且つめっき表面を最大粗さ（Ｒｍａｘ）で３０
μｍ未満とすることにより前記課題を達成したものであ
る。SUMMARY OF THE INVENTION In the present invention, 0.1-30% by weight of aluminum and 0.005-0.
In a hot-dip aluminum alloy plating containing 10% by weight and the balance being zinc except for impurities, Zn-
30 μm of alloy layer formed at the interface between Al layer and base steel
And the plated surface has a maximum roughness (Rmax) of 30.
By making the thickness less than μm, the above-mentioned object is achieved.
【０００９】このような本発明は、本発明者らが、先に
示した疲労特性低下要因である〜の何が真の原因で
あるかを鋭意検討した結果、得られたものであり、以下
にそれらを詳細に説明する。The present invention as described above has been obtained as a result of the inventors' earnestly examining what is the true cause of the above-mentioned factors that deteriorate the fatigue characteristics. They are explained in detail in.
【００１０】試験は各要因を単独に変化させながら平面
曲げ疲労試験を行い、疲労過程で生じるクラックの起点
の位置、疲労破断に至るまでのクラックの伝播の仕方を
観察することによって行った。この結果、以下の知見を
得た。The test was carried out by performing a plane bending fatigue test while changing each factor independently, and observing the position of the starting point of the crack generated in the fatigue process and the manner of propagation of the crack until fatigue fracture. As a result, the following findings were obtained.
【００１１】（１）合金層厚さが３０μｍ以上に発達し
た場合は、Ｆｅ−Ｚｎ，Ｆｅ−ＡｌあるいはＦｅ−Ａｌ
−Ｚｎの合金層内に存在する微細なボイド、クラック等
の欠陥部分ないしは最も硬度の高い鋼素地側の合金層と
鋼素地の界面に疲労初期クラックが現われ、表面側と鋼
素地側にクラックが伝播する。さらに、合金層と鋼素地
の界面では密着力の弱い界面に沿ったクラックも生成す
る。こうして最終的には破断に至る。表面に切欠効果と
なるような極端な欠陥が無ければ、表面には疲労起点は
見られない。(1) When the alloy layer has a thickness of 30 μm or more, Fe-Zn, Fe-Al or Fe-Al
-Defects such as fine voids and cracks existing in the Zn alloy layer, or fatigue initial cracks appear at the interface between the steel layer and the alloy layer on the steel base side having the highest hardness, and cracks occur on the surface side and the steel base side. Propagate. Further, at the interface between the alloy layer and the steel base, cracks are also generated along the interface with weak adhesion. This eventually leads to fracture. If there are no extreme defects on the surface that would cause a notch effect, no fatigue starting point is found on the surface.
【００１２】（２）合金層厚さが３０μｍ未満の場合に
は、（１）の場合以外に、めっき表面を起点とする場合
が見られ、両者が同時に観察される場合もある。表面に
起点を生じた場合には、クラックは粒界に沿って、合金
層、さらに鋼素地に達する。特に表面粗さが最大粗さ
（Ｒｍａｘ）で３０μｍ以上になった場合には、表面か
らのクラック発生が支配的である。(2) When the thickness of the alloy layer is less than 30 μm, in addition to the case of (1), the plating surface may be the starting point, and both may be observed at the same time. When the starting point is generated on the surface, the crack reaches the alloy layer and further the steel base along the grain boundary. In particular, when the surface roughness is 30 μm or more in terms of the maximum roughness (Rmax), crack generation from the surface is dominant.
【００１３】（３）なお、めっき条件及び冷却条件につ
いては、ａ）前処理の水素吸蔵の要因は排除できるもの
であり、ｂ）凝固時のめっき層の収縮による引張残留応
力の存在あるいはめっき表面の収縮によるマイクロクラ
ックとする要因は該当しないものである。(3) Regarding the plating conditions and cooling conditions, a) the factor of hydrogen absorption in the pretreatment can be eliminated, and b) the existence of tensile residual stress due to the contraction of the plating layer during solidification or the plating surface. The factors that cause microcracking due to the contraction of are not applicable.
【００１４】以上の知見から、合金層厚さを３０μｍ未
満に抑え、めっき表面粗さを最大粗さ（Ｒｍａｘ）で３
０μｍ未満に抑えることによって、素材に対して疲労限
度低下率が１５％未満の疲労特性の優れた溶融亜鉛アル
ミニウム合金めっき被覆物が得られることが判明した。From the above knowledge, the alloy layer thickness is kept to less than 30 μm, and the plating surface roughness is 3 in terms of the maximum roughness (Rmax).
It was found that by controlling the thickness to be less than 0 μm, a hot dip galvanized aluminum alloy coating having excellent fatigue properties with a fatigue limit reduction rate of less than 15% can be obtained.
【００１５】上記のような被覆物を得るには、例えば、
次のような条件の下で溶融めっきを行う。すなわち、 ａ）鋼材素材はできる限り平滑とする。 ｂ）めっき浴温度はめっき浴組成物の融点よりプラス２
０〜５０℃の範囲の一定温度（±５℃）に保ち、浸漬時
間はできる限り短くする。例えば５分以内とする。めっ
き浴温度がめっき浴組成物の融点より＋２０℃未満では
浴の粘度が上がり外観不良となる。また、＋５０℃以上
では合金層が発達し、３０μｍ以上となる。 ｃ）めっき引上時のワイピング条件は特に限定されない
が、均一なワイピングを行う必要がある。 ｄ）めっき後の冷却は、表面粗さを３０μｍ以上に粗く
しないように、均一に冷却することが必要である。合金
層が発達しなければ例えば６０℃／秒以下の徐冷側が望
ましい。なお、冷却速度が６０℃／秒を上回ると、表面
粗さが３０μｍ以上となり、不良めっきとなって疲労特
性が低下する。To obtain the above coating, for example,
Hot dip plating is performed under the following conditions. That is: a) The steel material should be as smooth as possible. b) The plating bath temperature is 2 above the melting point of the plating bath composition.
Maintain a constant temperature (± 5 ° C) in the range of 0 to 50 ° C, and make the immersion time as short as possible. For example, within 5 minutes. If the plating bath temperature is less than + 20 ° C above the melting point of the plating bath composition, the viscosity of the bath increases and the appearance becomes poor. Further, at + 50 ° C. or higher, the alloy layer develops and becomes 30 μm or more. c) Wiping conditions for pulling up the plating are not particularly limited, but it is necessary to perform uniform wiping. d) Cooling after plating needs to be uniformly performed so that the surface roughness is not roughened to 30 μm or more. If the alloy layer does not develop, the slow cooling side of, for example, 60 ° C./sec or less is desirable. If the cooling rate exceeds 60 ° C./sec, the surface roughness becomes 30 μm or more, resulting in poor plating and poor fatigue properties.
【００１６】以上の条件が主要な条件であり、他の条件
は合金層厚さや表面粗さに影響させない限り、大きな影
響は無い。The above-mentioned conditions are the main conditions, and the other conditions have no great influence unless they affect the alloy layer thickness and the surface roughness.
【００１７】例えば、その他の条件として、めっき方法
は直接めっきとしても、あるいは２度浸漬めっき方法
等、複数回のめっき、Ｚｎめっき後のＺｎ−Ａｌめっき
のいずれも可能である。また、直接Ｚｎ−Ａｌめっき
後、組成を変えた別種のＺｎ−Ａｌめっきを施すことも
できる。めっき浴組成として、公知の耐食性向上の目的
で皮膜脆性に影響しない範囲で微量のＭｇ添加、表面
性、濡れ性等の改善を目的としたミッシュメタル、その
他Ｌｉ，Ｓｂ，Ｃｕ，Ｎｉ等の添加も可能である。さら
に、めっき後の処理加工として、表面粗さの調整のため
に、めっき後に表面加工、スキンパス、研磨、加圧、化
学処理を行っても良い。なお、めっき層厚さについて
は、合金層厚ささえ厚くならなければ、めっき層が厚く
なっても疲労特性は低下せず、直接疲労特性には影響し
ない。通常、工業的に達成される１０〜１００μｍの広
い範囲にわたって、先の合金層厚さや表面粗さと疲労特
性の関係が成り立つ。For example, as other conditions, the plating method may be a direct plating method, a double immersion plating method, a plurality of times of plating, or Zn-Al plating after Zn plating. Further, it is also possible to directly perform Zn-Al plating and then perform another type of Zn-Al plating having a different composition. As a plating bath composition, a known amount of Mg is added for the purpose of improving corrosion resistance within a range that does not affect the film brittleness, misch metal for the purpose of improving surface properties, wettability, etc., and addition of Li, Sb, Cu, Ni, etc. Is also possible. Further, as the processing after plating, for the purpose of adjusting the surface roughness, surface processing, skin pass, polishing, pressurization, or chemical treatment may be performed after plating. Regarding the thickness of the plating layer, even if the thickness of the alloy layer is not increased, even if the thickness of the plating layer is increased, the fatigue characteristics are not deteriorated and the fatigue characteristics are not directly affected. Usually, the above-mentioned relationship between the alloy layer thickness and surface roughness and the fatigue property is established over a wide range of 10 to 100 μm which is industrially achieved.
【００１８】以下、実施例につき説明する。Examples will be described below.
【実施例】めっき素材として、一般構造用圧延鋼材ＳＳ
４１（分析結果、Ｃ：0.048wt%,Ｓｉ：0.018wt%,Ｍｎ：
0.330wt%,Ｃｒ：0.021wt%,Ｓ：0.009wt%）の同一ロット
から加工したＪＩＳＺ２２７５１号試験片（54W×110L
×1.2Tmm)の板であって、表面をＲｍａｘで１０〜１５
μｍに表面仕上げしたものを、通常のめっき前処理、す
なわち、アルカリ脱脂−水洗−酸洗（ＨＣｌ）−水洗−
フラックス処理−乾燥を施し、めっき浴に浸漬した。[Example] As a plating material, rolled steel SS for general structure
41 (analysis result, C: 0.048 wt%, Si: 0.018 wt%, Mn:
JISZ22751 test piece (54W × 110L) processed from the same lot of 0.330 wt%, Cr: 0.021 wt%, S: 0.009 wt%
× 1.2Tmm) plate, the surface of which is Rmax 10-15
What was surface-finished to μm is subjected to a normal plating pretreatment, that is, alkali degreasing-water washing-pickling (HCl) -water washing-
Flux treatment-dried, and immersed in a plating bath.
【００１９】めっき条件は、めっき浴組成として、純亜
鉛９９．９９５％浴と純亜鉛９９．９９５％亜鉛に９
９．９９％Ａｌ及びＮａを添加した浴を用いた。但し、
Ａｌが１０％以上の組成ではめっき浴中にＳｉを含有さ
せ、付着量を調整した。めっき温度は浴の融点＋２０〜
１００℃の範囲とし、浸漬時間は０．３〜１０分間の範
囲とした。The plating conditions are as follows: 9% pure zinc 99.995% bath and 9% pure zinc 99.995% zinc.
A bath containing 9.99% Al and Na was used. However,
When the composition of Al was 10% or more, Si was contained in the plating bath to adjust the adhesion amount. The plating temperature is the melting point of the bath + 20 ~
The temperature was set to 100 ° C. and the immersion time was set to 0.3 to 10 minutes.
【００２０】めっき浴からの引上げるときの冷却条件
は、水、油又はＮ2ガスにて調整して冷却速度２０〜１
００℃／秒の範囲とした。めっき後、光学顕微鏡により
疲労試験前後のめっき層断面観察とＳＥＭ観察、ＥＰＭ
Ａ観察を実施した。また、表面粗さは、粗さ計でめっき
表面の曲げを受ける部分全面にわたりＲｍａｘ等を測定
した。そして、疲労試験機は島津万能疲れ試験機ＵＦ−
１５形を用い、繰返し応力１５〜３０ｋｇｆ／ｍｍ
2（片振）、繰返し回数最大１０7回、平面曲げ試験と
し、実施した。これらの結果を次表に示す。The cooling conditions when pulling up from the plating bath are adjusted with water, oil or N 2 gas and the cooling rate is 20 to 1
The range was 00 ° C / sec. After plating, cross-section observation of plating layer and SEM observation before and after fatigue test by optical microscope, EPM
A observation was performed. As for the surface roughness, Rmax or the like was measured with a roughness meter over the entire surface of the plated surface that is bent. And the fatigue testing machine is Shimadzu Universal Fatigue Testing Machine UF-
15 type, repeated stress 15-30kgf / mm
2 (single swing), a maximum number of repetitions of 10 7 times, and a plane bending test were performed. The results are shown in the following table.
【００２１】[0021]
【表１】 [Table 1]
【００２２】以上の結果より、めっき温度、浸漬時間、
めっき後の冷却時間を選択し、合金層厚さ３０μｍ未満
とし、表面粗さＲｍａｘを３０μｍ未満に保つことによ
りめっき外観、疲労特性の優れためっき被覆物が得られ
ることが判る。From the above results, the plating temperature, immersion time,
It can be seen that by selecting the cooling time after plating, setting the alloy layer thickness to less than 30 μm and maintaining the surface roughness Rmax to less than 30 μm, a plated coating having excellent plating appearance and fatigue characteristics can be obtained.
【００２３】なお、めっき浴中に、０．００１〜０．１
重量％の範囲で、マグネシウム、リチウム、ミッシュメ
タル、ストロンチウム、銅又はニッケルの中から選ばれ
る１種又は２種以上を添加しても同様の結果が得られ
た。また、めっき素材をＳＰＣＣ冷延鋼板、鋼線に変更
した場合にも同様の結果が得られた。さらに、めっき方
式を次のように変更した場合にも先のめっき層全体厚
さ、合金層厚さ及び表面粗さの条件さえ満足すれば良好
な結果が得られることが判った。 １）亜鉛めっき後、再び亜鉛めっき、 ２）亜鉛めっき後、亜鉛アルミニウム合金めっき、 ３）亜鉛アルミニウム合金めっき後、再び亜鉛アルミニ
ウム合金めっき、 ４）亜鉛アルミニウム合金めっき後、Ａｌ等組成の異な
る亜鉛アルミニウム合金めっき。In the plating bath, 0.001-0.1
Similar results were obtained even if one or more selected from magnesium, lithium, misch metal, strontium, copper or nickel was added within the range of weight%. Similar results were obtained when the plating material was changed to SPCC cold rolled steel plate or steel wire. Further, it has been found that even when the plating method is changed as follows, good results can be obtained as long as the conditions of the total thickness of the plating layer, the thickness of the alloy layer and the surface roughness are satisfied. 1) After zinc plating, again zinc plating, 2) After zinc plating, zinc aluminum alloy plating, 3) After zinc aluminum alloy plating, again zinc aluminum alloy plating, 4) After zinc aluminum alloy plating, zinc aluminum with different composition such as Al Alloy plating.
【００２４】[0024]
【発明の効果】以上のように、本発明によれば、従来の
めっき方法の範囲で大幅な条件変更を伴わず、容易に操
業が可能で、微量のナトリウムを含有した溶融亜鉛アル
ミニウム合金めっき被覆物の利点である高耐食性及び外
観の良好さがそのまま保持され、しかもその疲労特性が
大幅に改善された溶融亜鉛アルミニウム合金めっき被覆
物が得られる。As described above, according to the present invention, it is possible to easily operate in the range of the conventional plating method without significantly changing the conditions, and the galvanized aluminum alloy plating coating containing a trace amount of sodium. It is possible to obtain a hot-dip zinc aluminum alloy plated coating which retains the advantages of high corrosion resistance and good appearance, which are the advantages of the product, and has significantly improved fatigue properties.
───────────────────────────────────────────────────── フロントページの続き (72)発明者 尾城 武司 埼玉県上尾市原市1333の２ 三井金属鉱業 株式会社総合研究所内 ─────────────────────────────────────────────────── ─── Continuation of front page (72) Inventor Takeshi Ogi 1333-3, Hara-shi, Ageo-shi, Saitama Mitsui Mining & Smelting Co., Ltd.
Claims (1)
リウム０．００５〜０．１０重量％を含有し、残部が不
純物を別にして亜鉛からなる溶融亜鉛アルミニウム合金
めっきにおいて、Ｚｎ−Ａｌ層と下地鋼材の界面に生成
する金属間化合物層を３０μｍ未満とし且つめっき表面
を最大粗さ（Ｒｍａｘ）で３０μｍ未満としたことを特
徴とする疲労特性に優れた溶融亜鉛アルミニウム合金め
っき被覆物。1. A molten zinc aluminum alloy plating containing 0.1 to 30% by weight of aluminum and 0.005 to 0.10% by weight of sodium, the balance being zinc except for impurities, and a Zn-Al layer. A hot-dip zinc aluminum alloy plated coating having excellent fatigue properties, characterized in that the intermetallic compound layer formed at the interface of the base steel material is less than 30 μm and the plating surface has a maximum roughness (Rmax) of less than 30 μm.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3236824A JP3009262B2 (en) | 1991-08-26 | 1991-08-26 | Hot-dip zinc aluminum alloy plating coating with excellent fatigue properties |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3236824A JP3009262B2 (en) | 1991-08-26 | 1991-08-26 | Hot-dip zinc aluminum alloy plating coating with excellent fatigue properties |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0551715A true JPH0551715A (en) | 1993-03-02 |
| JP3009262B2 JP3009262B2 (en) | 2000-02-14 |
Family
ID=17006330
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3236824A Expired - Fee Related JP3009262B2 (en) | 1991-08-26 | 1991-08-26 | Hot-dip zinc aluminum alloy plating coating with excellent fatigue properties |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3009262B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2001068932A1 (en) * | 2000-03-17 | 2001-09-20 | Nippon Steel Corporation | Plated metal wire and production method and production device therefor |
| KR20150126028A (en) * | 2013-03-07 | 2015-11-10 | 블루스코프 스틸 리미티드 | Channel inductor |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4409007B2 (en) * | 1999-10-12 | 2010-02-03 | 日新製鋼株式会社 | Method for producing highly corrosion-resistant hot-dip Zn-Al-Mg plated steel sheet with excellent surface properties |
| DE102007059015A1 (en) | 2007-12-06 | 2009-06-10 | Braun Gmbh | hairbrush |
| DE102007063154A1 (en) | 2007-12-29 | 2009-07-09 | Braun Gmbh | hairbrush |
-
1991
- 1991-08-26 JP JP3236824A patent/JP3009262B2/en not_active Expired - Fee Related
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2001068932A1 (en) * | 2000-03-17 | 2001-09-20 | Nippon Steel Corporation | Plated metal wire and production method and production device therefor |
| US6753479B2 (en) | 2000-03-17 | 2004-06-22 | Nippon Steel Corporation | Plated metal wire and method and apparatus for producing the same |
| KR20150126028A (en) * | 2013-03-07 | 2015-11-10 | 블루스코프 스틸 리미티드 | Channel inductor |
| JP2016515187A (en) * | 2013-03-07 | 2016-05-26 | ブルースコープ・スティール・リミテッドＢｌｕｅｓｃｏｐｅ Ｓｔｅｅｌ Ｌｉｍｉｔｅｄ | Groove type inductor |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3009262B2 (en) | 2000-02-14 |
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