JP2004002932A - Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the same - Google Patents
Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the same Download PDFInfo
- Publication number
- JP2004002932A JP2004002932A JP2002160167A JP2002160167A JP2004002932A JP 2004002932 A JP2004002932 A JP 2004002932A JP 2002160167 A JP2002160167 A JP 2002160167A JP 2002160167 A JP2002160167 A JP 2002160167A JP 2004002932 A JP2004002932 A JP 2004002932A
- Authority
- JP
- Japan
- Prior art keywords
- steel sheet
- plated steel
- plating
- aluminum
- intermetallic compound
- 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
Landscapes
- Coating With Molten Metal (AREA)
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と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】
従来、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。また、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。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。
【０００３】
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およ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、鋼板表面にＦｅ，Ａｌを主成分とする金属間化合物層が存在し、金属間化合物層の表面の粗度を制御することにより抵抗溶接性が改善することを見出した。そのメカニズムは明確では無いが以下のように推察される。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拡散して抑制されるが、アルミニウムめっき層がＦｅ−Ａｌ系の金属間化合物となって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というものである。
【０００７】
また、その金属間化合物層の表面粗度への抵抗溶接に対する影響としては、接触抵抗が変化することがあげられる。通常のめっき鋼板では通電初期では表面粗度の影響を受けるものの、その後はめっき層が溶融するために表面粗度の影響は比較的小さくなる。しかし、表面が金属間化合物層となっていると前述の如く溶接中のめっき層の溶融が抑制されるため、溶接中の板−電極間の接触抵抗は金属間化合物層の表面の状態に大きく影響される。
【０００８】
すなわち、粗度がＲａ０．５μｍ以上と大きい場合には電極−板間の通電点が確保されやすく接触抵抗が低下することが考えられる。接触抵抗が低下すると、電極表面での合金化反応が抑制されて電極寿命が大きく改善される。アルミニウムめっき鋼板を加熱してめっき層をＦｅ−Ａｌ合金とする知見は特開昭６０−２５１２６７号公報、特開２０００−３８６４０号公報、特開平９−１１８９７０号公報に示されているが、表面粗度の抵抗溶接性に及ぼす影響については言及しておらず、表面の粗度自体も開示されていない。
【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が存在し、金属間化合物の表面粗度がＲａ０．５μｍ以上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）鋼板表面の金属間化合物層にＳｉを含有することを特徴とする前記（１）に記載の抵抗溶接性に優れたアルミニウムめっき鋼板。
（３）前記（１）、（２）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。
鋼板表面にＦｅ，Ａｌを主成分とする金属間化合物層が存在するとしたのは、このような金属間化合物が表面に存在すると、抵抗溶接時のめっき層表面の溶融が抑制されてめっき金属が電極材料である銅合金と合金化しにくくなり、電極寿命が向上するためである。金属間化合物の表面粗度をＲａで０．５μｍ以上としたのは、これ以上の粗度であると電極−板間の通電点が多く確保されて接触抵抗が低下して電極寿命が顕著に向上するためである。粗度の上限については特に規定しないが、粗度が大きすぎるとチリ発生がしやすくなるため、３μｍ以下とした方が良い。
【００１１】
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。
【００１２】
通常、アルミめっき鋼板は溶融めっき法で製造されることが多く、このとき鋼板とめっき層の界面での金属間化合物層（合金層と称する）が成長しやすい。この層が成長しすぎると鋼板の加工性を損なうため、浴中にＳｉを１０％程度添加して製造されている。本発明においては、特に浴中にＳｉを添加する必要はないが、添加しても特に問題はない。めっき層の構成としては、Ａｌを主成分としているが、前述したようにＳｉの添加も可能である。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。
【００１３】
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。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。
【００１４】
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により左右されるため、金属間化合物層を形成する熱処理方法により検討するべきである。また、金属間化合物層の表面粗度を制御するためにいかなる方法をとっても良いが、以下の方法が推奨される。一つにはめっき原板となる冷延鋼板の粗度をＲａで０．５μｍ以上とすることである。冷延鋼板の粗度は冷延ロールの表面形状や圧延条件により制御される。
【００１５】
次には、高温に加熱する前のアルミニウムめっき鋼板の表面粗度をＲａで０．５μｍ以上とすることである。加熱前のアルミニウムめっき鋼板の表面粗度は、スキンパス圧延でのロールの表面形状などで制御できる。以上の２つの方法が生産性の点で優れる方法である。他の方法としては鋼板を高温に加熱して金属間化合物層を形成した後、ショットブラストなどにより表面粗度を形成してもよいが、前者の方法よりも生産性に劣るために少量生産には向いている。
【００１６】
めっき層中の金属間化合物を観察するためにはめっき層断面を研磨後にナイタール（エタノール＋２％硝酸）などで腐食すると、層構造が明確に分かる。それらの組成を測定するためには走査型電子顕微鏡などにて位置を特定した後、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）で組成を分析することが精度の点で望ましい。
【００１７】
【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。
【００１８】
【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。まためっき断面を研磨した後、ナイタール腐食し、走査型電子顕微鏡・エネルギー分散型Ｘ線分光計でめっき層観察と組成分析を行った。めっき層が金属間化合物であれば○、無ければ×という凡例で示す。
【００２２】
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。
【００２３】
（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
【００２４】
（評価基準）
○：連続打点５０００点以上
△：連続打点１０００点以上〜５０００点未満
×：連続打点１０００点未満
【００２５】
評価結果を表４、５、６にあわせて示す。本検討では１０００打点以上を良好とした。Ｎｏ．１、２、５、９、３２、３６、３７、４０、４４、６７、７１、７９、８５、９１はめっき層がＦｅ，Ａｌを主成分とする金属間化合物でなく、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．４、７、１１、１９、３０、３９、４２、４６、５４、６５は金属間化合物層の表面粗度が本発明の範囲外であるために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。
【００２６】
【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 by 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]
2. Description of the Related Art Conventionally, many automotive processed parts using thin steel plates are joined by resistance welding typified by spot welding in a vehicle body assembling process to form a vehicle body. Also, in recent years, the use of surface-treated steel sheets with plating applied to the surface of steel sheets 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. descend. 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. In spot welding, a phenomenon is observed in which the electrode tip diameter increases, the current density decreases, and no nugget is formed.
[0003]
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 steel sheet that shortens the electrode life during welding. As a technique for improving the electrode life of the aluminum-plated steel sheet, as disclosed in JP-A-10-183368, JP-A-10-46358, and JP-A-10-330957, In some cases, 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-described problem of weldability, and provides an aluminum-plated steel sheet having excellent resistance weldability and a machined 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, they found that an intermetallic compound layer mainly composed of Fe and Al was present on the steel sheet surface, and that resistance welding was improved by controlling the roughness of the surface of the intermetallic compound layer. The mechanism is not clear, but is presumed as follows. That is, the alloying of the plating metal and the copper alloy as the electrode is suppressed by the heat, which causes the plating metal to diffuse and is suppressed, but the aluminum plating layer becomes an Fe-Al-based intermetallic compound to raise the melting point. Melting of the surface is suppressed, and alloying is significantly suppressed.
[0007]
The effect of resistance welding on the surface roughness of the intermetallic compound layer includes a change in contact resistance. In the case of ordinary plated steel sheets, the surface roughness is affected at the beginning of energization, but thereafter, the influence of the surface roughness is relatively small because the plated layer is melted. However, if the surface is an intermetallic compound layer, the melting of the plating layer during welding is suppressed as described above, so that the contact resistance between the plate and the electrode during welding is large due to the state of the surface of the intermetallic compound layer. Affected.
[0008]
That is, when the roughness is as large as Ra 0.5 μm or more, it is conceivable that a conduction point between the electrode and the plate is easily secured and the contact resistance is reduced. When the contact resistance decreases, the alloying reaction on the electrode surface is suppressed, and the electrode life is greatly improved. The findings of heating an aluminum-plated steel sheet to form a plating layer of an Fe-Al alloy are disclosed in JP-A-60-251267, JP-A-2000-38640, and JP-A-9-1118970. No mention is made of the effect of roughness on resistance weldability, nor is the surface roughness itself disclosed.
[0009]
The gist of the present invention is as follows.
(1) An aluminum-plated steel sheet excellent in resistance weldability, characterized in that an intermetallic compound layer containing Fe and Al as main components is present on the surface of the steel sheet, and the surface roughness of the intermetallic compound is Ra 0.5 μm or more. .
(2) The aluminum-plated steel sheet excellent in resistance weldability according to (1), wherein the intermetallic compound layer on the surface of the steel sheet contains Si.
(3) A machined part using an aluminum-plated steel sheet excellent in resistance weldability, characterized by using the aluminum-plated steel sheet according to (1) or (2).
[0010]
BEST MODE FOR CARRYING OUT THE INVENTION
Hereinafter, the limitation range of the present invention will be described in detail.
The reason that the intermetallic compound layer mainly composed of Fe and Al is present on the surface of the steel sheet is that if such an intermetallic compound is present on the surface, the melting of the plating layer surface during resistance welding is suppressed, and the plating metal is formed. This is because it becomes difficult to alloy with the copper alloy as the electrode material, and the electrode life is improved. The reason why the surface roughness of the intermetallic compound is set to 0.5 μm or more in Ra is that if the roughness is higher than this, a large number of current-carrying points between the electrode and the plate are secured, the contact resistance is reduced, and the electrode life is remarkably increased. It is to improve. The upper limit of the roughness is not particularly specified, but if the roughness is too large, dust tends to be generated.
[0011]
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, are subjected to melting of the plating layer surface during resistance welding. Is suppressed, alloying between the plating metal and the electrode is suppressed, and heat generation is suppressed due to the low electric resistance of the surface of the plating layer, 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.
[0012]
Usually, an aluminum-plated steel sheet is often manufactured by a hot-dip plating method, and at this time, an intermetallic compound layer (referred to as an alloy layer) at an interface between the steel sheet and the plating layer tends to grow. If this layer grows too much, the workability of the steel sheet is impaired, so that it is manufactured by adding about 10% of Si to the bath. In the present invention, it is not particularly necessary to add Si to the bath, but there is no particular problem even if it is added. The configuration of the plating layer is mainly composed of Al, but Si can be added as described above. 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.
[0013]
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. 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.
[0014]
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. Since the composition of the surface depends on the heat treatment conditions, it should be examined by a heat treatment method for forming an intermetallic compound layer. Any method may be used to control the surface roughness of the intermetallic compound layer, but the following method is recommended. One is to set the roughness of the cold-rolled steel sheet as the plating base sheet to 0.5 μm or more in Ra. The roughness of the cold rolled steel sheet is controlled by the surface shape of the cold roll and the rolling conditions.
[0015]
Next, the surface roughness of the aluminum-plated steel sheet before heating to a high temperature should be 0.5 μm or more in Ra. The surface roughness of the aluminum-plated steel sheet before heating can be controlled by the surface shape of the roll in skin pass rolling. The above two methods are excellent in productivity. As another method, the steel plate may be heated to a high temperature to form an intermetallic compound layer, and then the surface roughness may be formed by shot blasting or the like. Is facing.
[0016]
In order to observe the intermetallic compound in the plating layer, the layer structure can be clearly understood by corroding the plating layer cross section with nital (ethanol + 2% nitric acid) after polishing. In order to measure the composition, it is necessary to specify the position using a scanning electron microscope or the like, and then analyze the composition using an electron beam microanalyzer (EPMA) or energy dispersive X-ray spectrometer (EDX). Is desirable.
[0017]
【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%.
[0018]
[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 ○. Further, after polishing the plating cross section, it was subjected to nital corrosion, and the plating layer was observed and the composition was analyzed using a scanning electron microscope and an energy dispersive X-ray spectrometer. If the plating layer is an intermetallic compound, it is indicated by a legend, and if not, X is indicated by a legend.
[0022]
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.
[0023]
(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 5000 points or more Δ: Continuous hit points of 1000 points or more to less than 5000 points ×: Continuous hit points of less than 1000 points
The evaluation results are shown in Tables 4, 5, and 6. In this study, 1000 points or more were determined to be good. No. The plating layers 1, 2, 5, 9, 32, 36, 37, 40, 44, 67, 71, 79, 85 and 91 are not intermetallic compounds whose main components are Fe and Al, and are outside the scope of the present invention. Therefore, melting of the plating layer surface was promoted, the electrode life was shortened, and the weldability was reduced. No. In 4, 7, 11, 19, 30, 39, 42, 46, 54 and 65, since the surface roughness of the intermetallic compound layer was out of the range of the present invention, the electrode life was shortened and the weldability was reduced. 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.
[0026]
[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 (3)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002160167A JP3843042B2 (en) | 2002-05-31 | 2002-05-31 | Aluminum-plated steel sheet with excellent resistance weldability and machined parts using it |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2002160167A JP3843042B2 (en) | 2002-05-31 | 2002-05-31 | Aluminum-plated steel sheet with excellent resistance weldability and machined parts using it |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2004002932A true JP2004002932A (en) | 2004-01-08 |
| JP3843042B2 JP3843042B2 (en) | 2006-11-08 |
Family
ID=30429679
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2002160167A Expired - Fee Related JP3843042B2 (en) | 2002-05-31 | 2002-05-31 | Aluminum-plated steel sheet with excellent resistance weldability and machined parts using it |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3843042B2 (en) |
Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008161878A (en) * | 2006-12-27 | 2008-07-17 | Nippon Steel Corp | Lap resistance spot welding method |
| JP2011137210A (en) * | 2009-12-28 | 2011-07-14 | Nippon Steel Corp | Steel sheet for hot stamp and method of producing the same |
| WO2018062341A1 (en) * | 2016-09-30 | 2018-04-05 | Ｊｆｅスチール株式会社 | Steel sheet for motorcycle fuel tank, and fuel tank member |
| WO2019011644A1 (en) * | 2017-07-10 | 2019-01-17 | Thyssenkrupp Steel Europe Ag | Method for producing a press-quenched part |
| JP2019073778A (en) * | 2017-10-18 | 2019-05-16 | 新日鐵住金株式会社 | Al-PLATED STEEL PIPE COMPONENT |
| WO2021162101A1 (en) | 2020-02-13 | 2021-08-19 | 日本製鉄株式会社 | Bonded component and method for producing same |
| JP2022106758A (en) * | 2017-06-01 | 2022-07-20 | ポスコ | Hot press molding steel sheet excellent in coating adhesion and after-painting corrosion resistance and method for manufacturing the same |
-
2002
- 2002-05-31 JP JP2002160167A patent/JP3843042B2/en not_active Expired - Fee Related
Cited By (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008161878A (en) * | 2006-12-27 | 2008-07-17 | Nippon Steel Corp | Lap resistance spot welding method |
| JP2011137210A (en) * | 2009-12-28 | 2011-07-14 | Nippon Steel Corp | Steel sheet for hot stamp and method of producing the same |
| WO2018062341A1 (en) * | 2016-09-30 | 2018-04-05 | Ｊｆｅスチール株式会社 | Steel sheet for motorcycle fuel tank, and fuel tank member |
| JP6354915B1 (en) * | 2016-09-30 | 2018-07-11 | Ｊｆｅスチール株式会社 | Steel plate and fuel tank member for motorcycle fuel tank |
| JP2022106758A (en) * | 2017-06-01 | 2022-07-20 | ポスコ | Hot press molding steel sheet excellent in coating adhesion and after-painting corrosion resistance and method for manufacturing the same |
| US11801664B2 (en) | 2017-06-01 | 2023-10-31 | Posco Co., Ltd. | Steel sheet for hot press formed member having excellent resistance to hydrogen delayed fracture and method for manufacturing thereof |
| US11820103B2 (en) | 2017-06-01 | 2023-11-21 | Posco Co., Ltd | Steel sheet for hot press formed member having excellent coating adhesion and manufacturing method for the same |
| JP7464649B2 (en) | 2017-06-01 | 2024-04-09 | ポスコホールディングス インコーポレーティッド | Steel sheet for hot press forming parts with excellent paint adhesion and corrosion resistance after painting, and its manufacturing method |
| WO2019011644A1 (en) * | 2017-07-10 | 2019-01-17 | Thyssenkrupp Steel Europe Ag | Method for producing a press-quenched part |
| JP2019073778A (en) * | 2017-10-18 | 2019-05-16 | 新日鐵住金株式会社 | Al-PLATED STEEL PIPE COMPONENT |
| WO2021162101A1 (en) | 2020-02-13 | 2021-08-19 | 日本製鉄株式会社 | Bonded component and method for producing same |
| KR20220124766A (en) | 2020-02-13 | 2022-09-14 | 닛폰세이테츠 가부시키가이샤 | Joint parts and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3843042B2 (en) | 2006-11-08 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP4724780B2 (en) | Aluminum-plated steel sheet for rapid heating hot press, manufacturing method thereof, and rapid heating hot pressing method using the same | |
| JP4695459B2 (en) | Hot pressed steel with zinc-based plating with excellent corrosion resistance after painting | |
| EP2794950B1 (en) | Hot-dip galvanized steel sheet having excellent adhesiveness at ultra-low temperatures and method of manufacturing the same | |
| JP7358542B2 (en) | Method for manufacturing alloyed hot-dip galvanized steel sheet resistant to liquid metal embrittlement | |
| JP2005113233A (en) | Zn-BASED PLATED STEEL FOR HOT PRESS | |
| JP7124991B1 (en) | Welded joints and auto parts | |
| JP7124992B1 (en) | Welded joints and auto parts | |
| JP7311041B2 (en) | Fe-based electroplated steel sheet, electrodeposition coated steel sheet, automobile parts, method for manufacturing electrodeposition coated steel sheet, and method for manufacturing Fe-based electroplated steel sheet | |
| KR20170118866A (en) | Hot-pressed member and manufacturing method therefor | |
| JP4551034B2 (en) | High-strength aluminum plated steel sheet for automobile parts with excellent weldability and post-painting corrosion resistance, and automobile parts using the same | |
| JP2004124207A (en) | Zn-PLATED STEEL SHEET FOR HOT-PRESS, AND CAR COMPONENTS WITH HIGH STRENGTH USING IT | |
| JP3843042B2 (en) | Aluminum-plated steel sheet with excellent resistance weldability and machined parts using it | |
| JP4720618B2 (en) | Alloyed hot-dip galvanized steel sheet and method for producing the same | |
| JP2004002931A (en) | Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the same | |
| JP7393551B2 (en) | Aluminum alloy plated steel sheet with excellent workability and corrosion resistance and its manufacturing method | |
| JP2002241916A (en) | Plated steel sheet having excellent corrosion resistance, workability and weldability and production method therefor | |
| JP2002241896A (en) | High strength galvanized steel sheet having excellent plating adhesion and press formability and production method therefor | |
| JP2004002933A (en) | Aluminum plated steel sheet having excellent resistance weldability and worked parts obtained by using the aluminum plated steel sheet | |
| JP6888743B1 (en) | Hot-pressed members, hot-pressed steel sheets, and their manufacturing methods | |
| JP2002371342A (en) | Hot-dip galvanized steel sheet and manufacturing method therefor | |
| JP2005048254A (en) | Galvanized steel having excellent film peeling resistance for hot forming | |
| JPH079074B2 (en) | Surface-treated steel sheet for electronic device parts | |
| JP6939825B2 (en) | Al-based galvanized steel sheet and its manufacturing method | |
| JP2938449B1 (en) | Hot-dip Sn-Zn plated steel sheet | |
| JP6939824B2 (en) | Al-based galvanized steel sheet and its manufacturing method |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20040902 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20050526 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20050607 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20051115 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20051212 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A821 Effective date: 20051214 |
|
| A911 | Transfer to examiner for re-examination before appeal (zenchi) |
Free format text: JAPANESE INTERMEDIATE CODE: A911 Effective date: 20060120 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20060328 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20060517 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20060627 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20060714 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20060808 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20060811 |
|
| R151 | Written notification of patent or utility model registration |
Ref document number: 3843042 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R151 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090818 Year of fee payment: 3 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100818 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100818 Year of fee payment: 4 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110818 Year of fee payment: 5 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20120818 Year of fee payment: 6 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130818 Year of fee payment: 7 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130818 Year of fee payment: 7 |
|
| S531 | Written request for registration of change of domicile |
Free format text: JAPANESE INTERMEDIATE CODE: R313531 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130818 Year of fee payment: 7 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130818 Year of fee payment: 7 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20130818 Year of fee payment: 7 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| S533 | Written request for registration of change of name |
Free format text: JAPANESE INTERMEDIATE CODE: R313533 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |
|
| LAPS | Cancellation because of no payment of annual fees |