JP2006218518A - Method for producing tailored blank material - Google Patents
Method for producing tailored blank material Download PDFInfo
- Publication number
- JP2006218518A JP2006218518A JP2005034937A JP2005034937A JP2006218518A JP 2006218518 A JP2006218518 A JP 2006218518A JP 2005034937 A JP2005034937 A JP 2005034937A JP 2005034937 A JP2005034937 A JP 2005034937A JP 2006218518 A JP2006218518 A JP 2006218518A
- Authority
- JP
- Japan
- Prior art keywords
- welding
- mass
- steel sheet
- plated steel
- corrosion resistance
- 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
- 239000000463 material Substances 0.000 title claims abstract description 46
- 238000004519 manufacturing process Methods 0.000 title claims description 11
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 72
- 239000010959 steel Substances 0.000 claims abstract description 72
- 238000007747 plating Methods 0.000 claims abstract description 53
- 238000003466 welding Methods 0.000 claims abstract description 44
- 229910018134 Al-Mg Inorganic materials 0.000 claims abstract description 20
- 229910018467 Al—Mg Inorganic materials 0.000 claims abstract description 20
- 210000001503 joint Anatomy 0.000 claims abstract description 17
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 11
- 239000000956 alloy Substances 0.000 claims abstract description 11
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 229910000861 Mg alloy Inorganic materials 0.000 claims description 2
- 230000008021 deposition Effects 0.000 claims 1
- 230000007797 corrosion Effects 0.000 abstract description 54
- 238000005260 corrosion Methods 0.000 abstract description 54
- 239000011324 bead Substances 0.000 abstract description 22
- 239000011248 coating agent Substances 0.000 abstract description 22
- 238000000576 coating method Methods 0.000 abstract description 22
- 239000010960 cold rolled steel Substances 0.000 abstract description 12
- 239000002184 metal Substances 0.000 abstract description 9
- 229910052751 metal Inorganic materials 0.000 abstract description 9
- 238000000034 method Methods 0.000 description 16
- 239000010408 film Substances 0.000 description 15
- 230000008961 swelling Effects 0.000 description 11
- 238000012360 testing method Methods 0.000 description 7
- 229910019142 PO4 Inorganic materials 0.000 description 6
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 6
- 239000010452 phosphate Substances 0.000 description 6
- 238000005304 joining Methods 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- 239000002131 composite material Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 230000004927 fusion Effects 0.000 description 4
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 4
- 238000000465 moulding Methods 0.000 description 4
- 238000004070 electrodeposition Methods 0.000 description 3
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- 229910007570 Zn-Al Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 239000008397 galvanized steel Substances 0.000 description 2
- 238000002844 melting Methods 0.000 description 2
- 230000008018 melting Effects 0.000 description 2
- 230000002265 prevention Effects 0.000 description 2
- 230000009471 action Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 230000001678 irradiating effect Effects 0.000 description 1
- 230000013011 mating Effects 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Images
Landscapes
- Arc Welding In General (AREA)
- Laser Beam Processing (AREA)
- Coating With Molten Metal (AREA)
Abstract
Description
本発明は、例えば絞り加工して自動車のボディや部品を製造する際の素材として好適なテーラードブランク材に関する。 The present invention relates to a tailored blank material suitable as a material for manufacturing a body or a part of an automobile by drawing, for example.
近年自動車用ボディ部品をプレス成形する際、材料歩留まりの向上，工程の簡素化、金型数の削減等を目的として、２種類以上の部品を一体成形する技術が採用されている。このような一体成形部品をプレス成形する素材、いわゆるテーラードブランク材としては、一般に板厚や材質の異なる鋼板を溶接接合されたものが用いられている。
テーラードブランク材は、強度が必要な部分にのみ高張力鋼板や板厚の厚い鋼板を使用して他の部位には強度の小さい鋼板や板厚の薄い鋼板を配置したり、耐食性が必要な部位にのみめっき鋼板を使用したりするといった適材適所の材料を配置した自動車ボディの構成を可能とする。このため、めっき鋼板や板厚の厚い鋼板を不必要に使用することがなくなり、大幅なコスト削減と車体重量の軽量化を図ることができる。
In recent years, when press-molding body parts for automobiles, a technique of integrally molding two or more types of parts has been adopted for the purpose of improving the material yield, simplifying the process, and reducing the number of dies. As a material for press-molding such an integrally molded part, so-called tailored blank material, generally, a steel plate having a different thickness or material is welded and joined.
For tailored blanks, high strength steel plates or thick steel plates are used only in areas where strength is required, and low strength steel sheets or thin steel plates are placed in other areas, or where corrosion resistance is required. This makes it possible to construct an automobile body in which the right material and the right material are used. For this reason, a plated steel plate or a thick steel plate is not used unnecessarily, and a significant cost reduction and weight reduction of the vehicle body can be achieved.
ところで、自動車分野では、走行中に泥水等が自動車の下側部分に付着して当該部分を錆やすくしていることから、自動車の下側部分には防錆能力の向上が望まれている。特に北米地域の自動車メーカは、自主規制として１０年，１５万マイル走行後の自動車ボディでの穴あき腐食保証を唱えているが、さらに保証年数，保証距離の延長化の動きもある。このため、穴あき腐食が起こりやすい部位、例えばフロアーパネルやサイドシルといったアンダーボディ部、或いはドアのヘム部やホイールハウスの合わせ部などといった部位での穴あき腐食対策の強化が課題となり、耐食性に優れためっき鋼板の使用が増加しようとしている。 By the way, in the automobile field, muddy water or the like adheres to the lower part of the automobile during traveling to make the part easy to rust. Automakers in North America, in particular, advocate for perforated corrosion guarantees in automobile bodies after driving for 150,000 miles for 10 years as a self-regulation, but there are also moves to extend the warranty years and warranty distance. For this reason, strengthening countermeasures against perforated corrosion in areas where perforated corrosion is likely to occur, such as underbody parts such as floor panels and side sills, door hem parts, and wheel house mating parts, is an issue and has excellent corrosion resistance. The use of galvanized steel is about to increase.
めっき鋼板を熱延鋼板や冷延鋼板と組合せてテーラードブランク材を製造する際、接合方法も問題となる。テーラードブランク材を構成するブランク材の接合方法としては、一般的に、レーザ溶接，プラズマ溶接のような溶融溶接法と、抵抗溶接法であるマッシュシーム溶接法があるが、めっき鋼板を部分的に用いたテーラードブランク材の場合には、めっき鋼板により電極輪の寿命が低下するため、マッシュシーム溶接法よりも溶融溶接法を用いることが多い。しかも溶接継手としては突合せ継手とする場合が多い。 When manufacturing a tailored blank material by combining a plated steel plate with a hot-rolled steel plate or a cold-rolled steel plate, the joining method also becomes a problem. Generally, there are fusion welding methods such as laser welding and plasma welding, and mash seam welding method, which is resistance welding method, as the joining method of the blank material constituting the tailored blank material. In the case of the used tailored blank material, the life of the electrode wheel is reduced by the plated steel plate, and therefore, the fusion welding method is often used rather than the mash seam welding method. Moreover, butt joints are often used as welded joints.
テーラードブランク材を溶融溶接法で製造しようとする際、生産性を高めるために各ブランク材を接合する溶接速度を高めることが試みられている。しかし、溶接速度を高めるためには、材料を十分に溶融・凝固させるために入熱エネルギを高める必要がある。すなわち、プラズマ溶接の場合には溶接電流を、レーザ溶接の場合にはレーザビーム出力を高める必要がある。
しかしながら、プラズマ溶接で溶接電流を過度に高めると高いアーク力によって溶融池を押し下げる量が異常に多くなってその部分に後方の溶融金属が充填しきれなかったり、またレーザ溶接でレーザビーム出力を過度に上げるとキーホールの深さが深くなりすぎて後方の溶融金属がキーホールを十分に充填しきれなくなったりしてしまう。これにより、溶接ビードがハンピング状態になったり、穴開き状態になったりして溶接不良が発生するという問題がある。
When trying to manufacture a tailored blank material by a fusion welding method, attempts have been made to increase the welding speed for joining the blank materials in order to increase productivity. However, in order to increase the welding speed, it is necessary to increase the heat input energy in order to sufficiently melt and solidify the material. That is, it is necessary to increase the welding current in the case of plasma welding and the laser beam output in the case of laser welding.
However, if the welding current is excessively increased by plasma welding, the amount of the molten pool pushed down by the high arc force becomes abnormally large, and the molten metal behind cannot be filled in that part, or the laser beam output is excessive by laser welding. If it is raised, the depth of the keyhole becomes too deep, and the molten metal behind cannot fully fill the keyhole. Thereby, there exists a problem that a welding bead will generate | occur | produce because a welding bead will be in a humping state or a hole opening state.
このような問題を解消するため、例えば特許文献１では、テーラードブランク材の構成材料の成分である鋼中のＣ或いはＳｉ量を変更する方法が提案されている。しかしながら、この方法は使用鋼種が限定される。或いはめっき母材のＳｉ量を増やそうとすると、Ｓｉがめっき密着性を低下させるという問題が生じる。
このため、溶接ビードの安定性以外にも溶接後の加工性やめっき鋼板製造時の安定性等を考慮して成分設計しなければならないことはもとより、鋼材の製造時に非常に細かい成分調整をしなければならないため鋼材製造時の効率低下，歩留まり低下を招いて、結果としてコストの高い材料となってしまう。
For this reason, in addition to the stability of the weld bead, it is necessary to design the components in consideration of the workability after welding and the stability during the manufacture of the plated steel sheet, etc. Therefore, the efficiency and the yield at the time of manufacturing the steel material are reduced, resulting in a high cost material.
一方、自動車部品であって、耐食性を必要とするものには通常亜鉛めっき鋼板が用いられているが、さらなる穴あき腐食対策としては、めっき付着量の増加やシーラ或いはワックスを塗布する２次防錆による防錆強化が挙げられる。しかしながら、シーラやワックスを塗布しようとすると、自動車部材等では穴あき腐食が懸念される部位である隙間部や袋構造部が多く、それらの部位への塗布を人手を介して行うことは困難を極める。また塗布が手探り状態で行われるためシールが不十分な場合もある。さらにめっき付着量の増加やシーラやワックスを塗布するために、材料コストや副資材コストが増加することも問題となる。
本発明は、このような問題を解消すべく案出されたものであり、突合せ継手溶接時の入熱エネルギを大きくしても安定した溶接ビードが得られるとともに、絞り加工性や耐穴あき腐食性に優れたテーラードブランク材を低コストで提供することを目的とする。
On the other hand, galvanized steel sheets are usually used for automobile parts that require corrosion resistance. However, as a countermeasure against further perforated corrosion, an increase in the amount of plating adhesion or secondary protection by applying a sealer or wax is used. Rust prevention reinforcement by rust is mentioned. However, when applying sealer or wax, there are many gaps and bag structure parts that are likely to be perforated in automobile parts, etc., and it is difficult to apply these parts manually. I will master it. Moreover, since application | coating is performed in a groping state, a seal | sticker may be inadequate. Furthermore, the increase in the amount of plating and the increase in material cost and sub-material cost due to the application of sealer and wax are also problematic.
The present invention has been devised to solve such problems, and a stable weld bead can be obtained even when the heat input energy at the time of butt joint welding is increased, as well as drawing workability and perforated corrosion resistance. It aims at providing tailored blank material excellent in property at low cost.
本発明のテーラードブランク材の製造方法は、その目的を達成するため、互いに異なる鋼板を溶接接合してテーラードブランク材を製造する際に、一方の鋼板として、３〜１５質量％のＡｌ，２〜５質量％のＭｇ，必要に応じてさらに０．５質量％以下のＳｉを含み、残部がＺｎと不可避的不純物からなるＺｎ−Ａｌ−Ｍｇ系合金めっき層を片面当り２０ｇ／ｍ2以上の付着量でその両面に有するめっき鋼板を用い、その端部を他の鋼板の端部と突合せ、当該突合せ継手部をレーザビーム溶接又はプラズマ溶接することを特徴とする。 In order to achieve the object, the method for producing a tailored blank material according to the present invention, when producing a tailored blank material by welding and joining different steel plates, 3 to 15% by mass of Al, 2 to Adhering a Zn-Al-Mg-based alloy plating layer containing 5% by mass of Mg and optionally 0.5% by mass or less of Si and the balance of Zn and inevitable impurities to 20 g / m 2 or more per side It is characterized in that a plated steel plate having both sides is used in an amount, its end is butted against the end of another steel plate, and the butt joint is laser beam welded or plasma welded.
本発明では、テーラードブランク材を構成するめっき鋼板として、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板を用いることにより、突合せ継手部を溶融溶接する際に形成される溶接ビードの安定性がよく、入熱エネルギを高くすることが可能となるので生産性が向上する。
また、突合せ継手溶接されたテーラードブランク材は、絞り加工性に関しては従来品と同程度であるが、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき層に基づく優れた耐穴あき腐食性や耐塗膜膨れ腐食性を有しているため、その後絞り加工された自動車部品等の高性能化に貢献することができる。
In the present invention, by using a molten Zn-Al-Mg alloy-plated steel sheet as the plated steel sheet constituting the tailored blank material, the stability of the weld bead formed when the butt joint is melt welded is improved. Since the heat energy can be increased, productivity is improved.
In addition, tailored blanks that have been butt-welded are similar to conventional products in terms of drawing workability, but have excellent perforated corrosion resistance and coating swell resistance based on the molten Zn-Al-Mg alloy plating layer. Since it has corrosiveness, it can contribute to the performance enhancement of the automotive parts etc. which were drawn after that.
本発明者等は、２種類以上の部品を一体的にプレス成形する際に用いられるテーラードブランク材として、溶接時に形成される溶接ビードの安定性と製造されたテーラードブランク材の絞り加工性並びに耐穴あき腐食性等の向上策について種々検討した。
まず、防錆力向上の目的からめっき鋼板が用いられているテーラードブランク材は、例えばセンターピラーのように、厳しい耐食性が要求される下側部分にめっき鋼板が用いられ、他の部分に冷延鋼板が用いられている。そこで、耐穴あき腐食性等の向上策として、通常用いられている合金化溶融Ｚｎめっき鋼板（ＧＡ）や溶融Ｚｎめっき鋼板（ＧＩ）よりも優れた耐食性を有するめっき鋼板の使用が想定される。
As a tailored blank material used when integrally pressing two or more types of parts, the present inventors have made the stability of the weld bead formed during welding and the drawability and resistance of the manufactured tailored blank material. Various measures for improving perforated corrosivity were studied.
First, tailored blank materials that use plated steel sheets for the purpose of improving rust prevention power use plated steel sheets in the lower part where strict corrosion resistance is required, such as center pillars, and cold-roll in other parts. A steel plate is used. Therefore, as an improvement measure such as perforated corrosion resistance, use of a plated steel sheet having corrosion resistance superior to that of a commonly used alloyed hot-dip Zn-plated steel sheet (GA) or hot-dip Zn-plated steel sheet (GI) is assumed. .
本出願人等は、前記ＧＡやＧＩよりも優れた耐食性を有するめっき鋼板として、Ａｌ，Ｍｇ及び必要に応じてさらにＳｉを含み、残部がＺｎ及び不可避的不純物からなる溶融Ｚｎ−Ａｌ−Ｍｇ系の合金めっき浴を用いて溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっきを施した鋼板を提案してきた（例えば、特開２００２−２２６９５８号公報参照）。
本発明も、基本的には上記で提案のめっき鋼板を用いるものである。
素材の一部にめっき鋼板を用いてテーラードブランク材を接合する際には、前記したように、継手として突合せ継手を採用し、溶接法としてレーザ溶接，プラズマ溶接のような溶融溶接法を採用する。本発明でも、従来どおり、突合せ継手部を溶融溶接する手法を採用する。
The present applicants, as a plated steel sheet having corrosion resistance superior to GA and GI, include Al, Mg and, if necessary, further Si, and a molten Zn—Al—Mg system composed of Zn and inevitable impurities. Steel plates that have been subjected to hot-dip Zn—Al—Mg alloy plating using an alloy plating bath have been proposed (see, for example, JP-A-2002-226958).
The present invention also basically uses the above-mentioned proposed plated steel sheet.
When joining a tailored blank using a plated steel plate as a part of the material, as described above, a butt joint is adopted as a joint, and a fusion welding method such as laser welding or plasma welding is adopted as a welding method. . Also in the present invention, the technique of melting and welding the butt joint portion is employed as usual.
ところで、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板を普通の熱延鋼板や冷延鋼板と突合せ、突合せ継手溶接してテーラードブランク材を製造する際には、溶接性やその後のプレス加工性或いは実際に自動車部品として使用する際の耐穴あき腐食性等の特性と、めっき層の組成やめっき付着量との関係を予め検討する必要がある。
そこで、まずめっき層の組成と溶接性の関係を検討した。
前記したようにセンターピラー等を絞り加工する際に用いられるテーラードブランク材としては、材料特性やコスト等を考慮してめっき鋼板と冷延鋼板とを組合せたものが多いことから、上記検討においても、めっき鋼板と組合せる鋼板として通常の冷延鋼板を採用した。
By the way, when producing a tailored blank material by butt-welding a molten Zn-Al-Mg alloy-plated steel sheet with a normal hot-rolled steel sheet or cold-rolled steel sheet and welding a butt joint, the weldability and the subsequent press workability or actual In addition, it is necessary to examine in advance the relationship between characteristics such as perforation corrosion resistance when used as an automobile part, the composition of the plating layer, and the amount of plating deposited.
Therefore, first, the relationship between the composition of the plating layer and weldability was examined.
As described above, the tailored blank material used when drawing the center pillar or the like is often a combination of a plated steel plate and a cold-rolled steel plate in consideration of material properties, cost, etc. A normal cold-rolled steel sheet was adopted as a steel sheet to be combined with the plated steel sheet.
めっき鋼板として、片面当りの付着量が６０ｇ／ｍ2の溶融Ｚｎ−６質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板と、片面当りの付着量が６０ｇ／ｍ2の合金化溶融Ｚｎめっき鋼板（ＧＡ）を用いた。なお、めっき鋼板及び冷延鋼板としては、いずれも板厚が０．８ｍｍのものを用いた。上記２種のめっき鋼板１を、それぞれ図１に示すように冷延鋼板２と突合せ、継手部３をレーザ４で溶接した。そして、レーザビームの出力とビードの形状との関係をみた。その結果を図２に示す。
溶接ビードがハンピング状態や穴開き状態となって不良形状となる最大レーザビーム出力は、冷延鋼板と溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板の方が、冷延鋼板とＧＡの組合せよりも高いことがわかる。すなわち、最大レーザビーム出力を高くしても、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板との組合せの方が、正常な溶接ビードを維持しやすいことがわかる。最大レーザビーム出力を高くすることは、溶接速度を早くすることにつながり、結果的に生産効率が向上できることになる。
As plated steel sheet, hot-dip Zn-6 mass% Al-3 mass% Mg alloy plated steel sheet and the amount deposited per one side of 60 g / m 2 alloyed hot-dip Zn plated steel sheet adhesion amount 60 g / m 2 per one side ( GA) was used. In addition, as a plated steel plate and a cold-rolled steel plate, those with a plate thickness of 0.8 mm were used. The two types of plated
The maximum laser beam power at which the weld bead is in a humped state or a holed state and becomes a defective shape is higher in the cold-rolled steel plate and the molten Zn-Al-Mg alloy-plated steel plate than in the cold-rolled steel plate and GA I understand that. That is, even if the maximum laser beam output is increased, it can be seen that the combination with the molten Zn—Al—Mg alloy-plated steel sheet tends to maintain a normal weld bead. Increasing the maximum laser beam output leads to an increase in welding speed, and as a result, production efficiency can be improved.
溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板との組合せの方が、正常な溶接ビードが形成されやすい現象は、溶接時にめっき層のＡｌが溶融池に混入し、溶融金属の粘性を下げて流動しやすい状態に変質させるため、レーザビームが高出力化してキーホール深さが増大しても、後方の溶融金属がキーホールを充填しやすくなっていることによるものと推測される。
また、この作用は、プラズマ溶接の際にも同様に発現する。溶接電流を高くして溶融池を過度に押し下げても、その部分に後方の溶融金属が容易に流入して溶融池を充満させ、正常な溶接ビードを形成するものと推測される。
The phenomenon that a normal weld bead is more likely to be formed in combination with a molten Zn-Al-Mg alloy-plated steel sheet is that Al in the plating layer is mixed into the molten pool during welding, and the viscosity of the molten metal decreases and flows. Even if the laser beam is increased in power and the keyhole depth is increased in order to change to an easy state, it is presumed that the molten metal behind tends to fill the keyhole.
This effect is also manifested during plasma welding. Even if the welding current is increased and the molten pool is pushed down excessively, it is presumed that the molten metal behind easily flows into the portion to fill the molten pool and form a normal weld bead.
次に、上記２種のテーラードブランク材の絞り加工性について検討した。
それぞれ、突合せ継手溶接部分が中心になるようにブランクし、カップ加工による限界絞り比（Ｌ．Ｄ．Ｒ）の測定を行った。その結果を図３に示す。
溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板と冷延鋼板を組合せたサンプルの絞り加工性は、ＧＡと冷延鋼板を組合せたサンプルの絞り加工性と比べて同等以上であることがわかる。溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき層を形成した鋼板を用いたテーラードブランク材であっても、特殊な金型形状や成形条件を採用する必要はなく、従来から用いられているＧＡ材と同様に絞り加工することが可能である。
Next, the drawability of the two types of tailored blank materials was examined.
Each was blanked so that the welded portion of the butt joint was at the center, and the limit drawing ratio (LDR) was measured by cup processing. The result is shown in FIG.
It can be seen that the drawability of the sample combining the hot-dip Zn—Al—Mg alloy-plated steel plate and the cold-rolled steel plate is equal to or greater than the drawability of the sample combining the GA and the cold-rolled steel plate. Even if it is a tailored blank material using a steel plate on which a molten Zn-Al-Mg alloy plating layer is formed, it is not necessary to adopt a special mold shape or molding conditions, and it is the same as that of a GA material used conventionally. Can be drawn.
さらに、上記２種のテーラードブランク材の耐食性について検討することになるが、自動車部品等において、耐食性を必要とする箇所にのみめっき鋼板が配置されているので、テーラードブランク材全体についての耐食性は検討する必要がない。そこで、２種のめっき鋼板についての耐食性を検討した。また、自動車部品等にあっては電着塗装された状態で使用されている。そして腐食されやすい部位が、通常電着塗膜が付き廻りにくい袋構造部等であることを考慮し、リン酸塩処理後に電着塗膜の膜厚を５μｍと、一般的な評価時よりも膜厚を薄くしたテストピースを作製し、ＪＩＳ Ｈ８５０２に準じた複合腐食試験を行って、耐穴あき腐食性を調査した。 Furthermore, the corrosion resistance of the above two types of tailored blank materials will be examined. However, in automobile parts, etc., the corrosion resistance of the tailored blank materials as a whole is examined because the plated steel sheets are arranged only in places where corrosion resistance is required. There is no need to do. Therefore, the corrosion resistance of the two types of plated steel sheets was examined. In addition, automobile parts and the like are used in an electrodeposited state. Considering that the part that is easily corroded is usually a bag structure part where the electrodeposition coating film is difficult to attach, the film thickness of the electrodeposition coating film after phosphate treatment is 5 μm, which is higher than the general evaluation time. A test piece having a thin film thickness was prepared, and a composite corrosion test according to JIS H8502 was conducted to investigate perforated corrosion resistance.
図４は、板厚が０．７ｍｍで、片面当りのめっき付着量が６０ｇ／ｍ2の溶融Ｚｎ−６質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板と、片面当りの付着量が６０ｇ／ｍ2の合金化溶融Ｚｎめっき鋼板（ＧＡ）並びに溶融Ｚｎめっき鋼板（ＧＩ）についての、穴あき腐食に到るまでのサイクル数を示したものである。
ＧＡをベースにしたものでは２４０サイクルで、ＧＩをベースにしたものでは２８０サイクルで穴あき腐食に到っているのに対して、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板をベースにしたものにあっては５００サイクル終了後も穴あき腐食は発生していなかった。
FIG. 4 shows a molten Zn-6 mass% Al-3 mass% Mg alloy-plated steel sheet having a plate thickness of 0.7 mm and a plating adhesion amount per side of 60 g / m 2 , and an adhesion amount per side of 60 g / m. 2 shows the number of cycles to reach perforated corrosion for the alloyed hot-dip Zn-plated steel plate (GA) and hot-dip Zn-plated steel plate (GI).
In the case of the GA-based one, 240 cycles, and in the case of the GI-based one, the pierced corrosion is reached in 280 cycles, while the one based on the molten Zn-Al-Mg alloy-plated steel sheet. In that case, no perforated corrosion occurred even after 500 cycles.
さらにまた、外観を問われる部位への適用を想定し、傷が付いた塗膜部の塗膜膨れ腐食を調査した。
板厚が０．７ｍｍで、片面当りのめっき付着量が６０ｇ／ｍ2の溶融Ｚｎ−６質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板と、片面当りのめっき付着量が６０ｇ／ｍ2の溶融Ｚｎ−１８質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板並びに片面当りの付着量が６０ｇ／ｍ2の合金化溶融Ｚｎめっき鋼板（ＧＡ）をベースに、リン酸塩処理後に電着塗膜の膜厚を２０μｍに調整したテストピースを作製し、ＪＩＳ Ｈ８５０２に準じた複合腐食試験を行って、クロスカット部からの塗膜膨れ幅を調査した。
１００サイクル後の塗膜膨れ幅は、溶融Ｚｎ−６質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板と合金化溶融Ｚｎめっき鋼板（ＧＡ）では、ともにほぼ同等の２ｍｍ以下であったが、溶融Ｚｎ−１８質量％Ａｌ−３質量％Ｍｇ合金めっき鋼板では５ｍｍ以上を示し、耐塗膜膨れ腐食性に劣っていた。めっき層中のＡｌ量が多すぎると却って耐塗膜膨れ腐食性を低下させることがわかる。
Furthermore, the coating film swelling corrosion of the scratched coating film part was investigated supposing the application to the site | part which asks an external appearance.
Molten Zn-6 mass% Al-3 mass% Mg alloy-plated steel sheet with a plate thickness of 0.7 mm and a plating adhesion amount per side of 60 g / m 2, and a melting rate of plating adhesion amount per side of 60 g / m 2 Based on Zn-18 mass% Al-3 mass% Mg alloy-plated steel sheet and alloyed hot-dip Zn-plated steel sheet (GA) with an adhesion amount per side of 60 g / m 2 , an electrodeposition coating film after phosphate treatment A test piece having a thickness adjusted to 20 μm was prepared, and a composite corrosion test according to JIS H8502 was conducted to investigate the swollen width of the coating film from the crosscut portion.
The swollen width of the coating film after 100 cycles was approximately equal to 2 mm or less for both the molten Zn-6 mass% Al-3 mass% Mg alloy-plated steel sheet and the alloyed molten Zn-plated steel sheet (GA). The -18 mass% Al-3 mass% Mg alloy-plated steel sheet showed 5 mm or more, and was inferior in coating film swelling corrosion resistance. It can be seen that when the amount of Al in the plating layer is too large, the coating film swelling and corrosion resistance is lowered.
溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板は、そのめっき層の組成によって特性が変化する。したがって、その成分組成は、溶融溶接性及びその後使用される場合の耐穴あき腐食性や耐塗膜膨れ腐食性を考慮して決められる。
適正量のＡｌとＭｇを含む溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっきを施した鋼板は、めっき層が腐食すると、ＡｌとＭｇを含んだＺｎ腐食生成物が生成し、その腐食生成物がＡｌとＭｇにより安定化するため防食効果がたかまり、耐穴あき腐食性が向上する。また、例えば自動車ボディのように塗装前処理であるリン酸塩処理を行ったときに、溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板のめっき層は、主にＺｎとＡｌとＭｇが微細に分散した三元共晶組織から成ることから、そのめっき層上には微細で緻密なリン酸塩結晶が析出し、ＺｎとＡｌから成る従来の溶融Ｚｎ−Ａｌ系合金めっき鋼板では劣っていた耐塗膜膨れ腐食性も満足できるものとなる。
The characteristics of the hot-dip Zn—Al—Mg alloy-plated steel sheet vary depending on the composition of the plating layer. Therefore, the component composition is determined in consideration of the melt weldability, the perforation corrosion resistance and the coating film swelling corrosion resistance when used thereafter.
When the plated layer is corroded, the steel sheet subjected to hot-dip Zn-Al-Mg alloy plating containing appropriate amounts of Al and Mg produces a Zn corrosion product containing Al and Mg, and the corrosion product is Al and Mg. Since it is stabilized by Mg, the anticorrosion effect is increased and the perforated corrosion resistance is improved. In addition, for example, when a phosphate treatment, which is a pre-painting treatment, is performed as in an automobile body, the plating layer of a hot-dip Zn—Al—Mg alloy-plated steel sheet mainly contains finely dispersed Zn, Al, and Mg. Because it consists of a ternary eutectic structure, fine and dense phosphate crystals are deposited on the plated layer, which is inferior to conventional molten Zn-Al alloy-plated steel sheets made of Zn and Al. The swelling and corrosiveness can be satisfied.
詳細は後記の実施例に譲るが、その限定理由を次に記す。
Ａｌ：３〜１５質量％
溶融めっき金属の粘性を下げて良好な溶接ビードを保つためには、めっき層中のＡｌとしては３質量％以上が必要である。一方、Ａｌ量の増加は溶接ビードに対しては良好に働くものの、めっき層中やめっき表面でのＡｌ相の占める割合が増えることから、自動車ボディ等に使用する際の塗装前処理であるリン酸塩処理性を阻害して塗膜膨れ耐食性を低下させる。このため、めっき層中のＡｌ量は１５質量％以下、好ましくは１０質量％以下にする。
Details will be given in the examples described later, and the reasons for limitation will be described below.
Al: 3 to 15% by mass
In order to maintain the good weld bead by lowering the viscosity of the hot dip metal, 3% by mass or more is required as Al in the plating layer. On the other hand, the increase in Al content works well for weld beads, but since the proportion of Al phase in the plating layer and the plating surface increases, it is a coating pretreatment when used for automobile bodies, etc. It inhibits acid-treating ability and lowers coating film swelling and corrosion resistance. For this reason, the amount of Al in the plating layer is 15% by mass or less, preferably 10% by mass or less.
Ｍｇ：２〜５質量％
良好な耐穴あき腐食性を得るためには、めっき層中のＭｇ量は２質量％以上にする必要がある。Ｍｇの添加は耐穴あき腐食性を向上させるばかりでなく、リン酸塩処理性に対しても効果を発揮する。すなわち、ＡｌとＭｇが複合添加されると、同量のＡｌを単独で添加したＺｎ−Ａｌ系のめっき層と比べてリン酸塩処理性が改善され、耐塗膜膨れ腐食性が良好になる。一方、Ｍｇ添加量が多くなりすぎると、めっき層中にＺｎ2Ｍｇ相が現れるようになる。Ｚｎ2Ｍｇ相はＺｎ相と比較して電位的に卑であることから、めっき層中で優先的に腐食する。そのため、Ｚｎ2Ｍｇ相の出現量が多いほど、すなわちＭｇ添加量が過度になるほど、めっき層内で優先腐食する部分が増え、耐塗膜膨れ腐食性が低下する。Ｚｎ2Ｍｇ相の出現限界がＭｇ：５質量％であるから、めっき層中のＭｇ量は５質量％以下とする。
さらに、Ｚｎ2Ｍｇ相の出現を抑える目的で、めっき層中にはＴｉ，Ｂを０．０１質量％以下の割合で適宜添加しても良い。
Mg: 2 to 5% by mass
In order to obtain good perforated corrosion resistance, the amount of Mg in the plating layer needs to be 2% by mass or more. The addition of Mg not only improves the perforated corrosion resistance, but also has an effect on the phosphate treatment ability. That is, when Al and Mg are added in combination, phosphate treatment properties are improved and coating film swelling and corrosion resistance is improved as compared with a Zn-Al-based plating layer in which the same amount of Al is added alone. . On the other hand, if the amount of Mg added is too large, a Zn 2 Mg phase appears in the plating layer. Since the Zn 2 Mg phase is lower in potential than the Zn phase, it corrodes preferentially in the plating layer. Therefore, the more the Zn 2 Mg phase appears, that is, the more Mg is added, the more preferential corrosion occurs in the plating layer, and the coating swelling swelling resistance decreases. Since the appearance limit of the Zn 2 Mg phase is Mg: 5% by mass, the amount of Mg in the plating layer is set to 5% by mass or less.
Furthermore, in order to suppress the appearance of the Zn 2 Mg phase, Ti and B may be appropriately added to the plating layer at a ratio of 0.01% by mass or less.
Ｓｉ：０．５質量％以下
Ｓｉは、Ａｌと複合添加されるとき、良好な溶接ビード状態を形成する作用を有する。一方、０．５質量％を超える添加は、めっき層中やめっき表面でＳｉの金属間化合物を形成し、Ａｌと同様にリン酸塩処理性を阻害して耐塗膜膨れ腐食性を低下させる。したがって、Ｓｉを含ませる場合には、０．５質量％以下とする。
めっき付着量が少ないと良好な耐穴あき腐食性と溶接ビード状態を得る上で、形成しためっき層の効果が発現しないので、片面当り２０ｇ／ｍ2以上の付着量でめっきする必要がある。
Si: 0.5% by mass or less Si, when added in combination with Al, has an action of forming a good weld bead state. On the other hand, addition exceeding 0.5% by mass forms an intermetallic compound of Si in the plating layer or on the plating surface and, like Al, inhibits phosphatability and lowers coating film swelling and corrosion resistance. . Therefore, when Si is included, the content is 0.5% by mass or less.
When the amount of plating is small, the effect of the formed plating layer is not exhibited in obtaining good perforated corrosion resistance and weld bead state. Therefore, it is necessary to perform plating with an amount of adhesion of 20 g / m 2 or more per side.
板厚が一定の０．８ｍｍとし、付着量とめっき層中の組成を種々変えた溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板を準備し、ＹＡＧレーザを用いて同板厚の冷延鋼板との突合せ継手溶接を、図１に示すように、めっき鋼板と冷延鋼板の突合せ位置にレーザビームを照射して行った。
このとき、レーザビーム出力は３．５ｋＷに統一し、他は表１に示す条件とした。
溶接サンプルの評価は、溶接ビード形成状態，表２に示す条件で実施した絞り加工性，及び前述したのと同様の穴あき腐食と塗膜膨れ腐食の塗装後耐食性試験を行った。
Prepare a hot-dip Zn-Al-Mg alloy-plated steel sheet with a constant plate thickness of 0.8 mm and various amounts of adhesion and composition in the plating layer. As shown in FIG. 1, butt joint welding was performed by irradiating a butt position between a plated steel plate and a cold-rolled steel plate with a laser beam.
At this time, the laser beam output was unified to 3.5 kW, and other conditions were as shown in Table 1.
The weld samples were evaluated by conducting post-coating corrosion resistance tests of the weld bead formation state, the drawability performed under the conditions shown in Table 2, and the same perforation corrosion and paint swell corrosion as described above.
それらの結果をまとめて表３に示す。
なお、表３中の溶接ビード状態は、ハンピングや穴開きがなかったものを◎で、ハンピングや穴開きがあったものを×で示している。耐穴あき腐食性は、ＪＩＳ Ｈ８５０２による複合腐食試験を５００サイクル行っても穴あき腐食しなかったものを◎で、４９９〜３００サイクルで穴あき腐食したものを○で、３００サイクル未満で穴あき腐食したものを×で示している。耐塗膜膨れ腐食性は、ＪＩＳ Ｈ８５０２による複合腐食試験を１００サイクル行った後、クロスカット部からの塗膜膨れ幅を測定し、その幅が３ｍｍ未満のものを◎で、３ｍｍ以上〜５ｍｍ未満のものを○で、５ｍｍ以上のものを×で示している。
また、表３中、Ｎｏ．９は溶融Ｚｎ−Ａｌ−Ｍｇ系合金めっき鋼板とＧＡ材の突合せ継手溶接、Ｎｏ．１８は、ＧＡ材同士の突合せ継手溶接の結果を示したものである。
The results are summarized in Table 3.
In Table 3, the weld bead state is indicated by ◎ when there is no humping or perforation, and by × when there is humping or perforation. The perforated corrosion resistance is ◎ for those that did not undergo perforation corrosion even after performing 500 cycles of the composite corrosion test according to JIS H8502, and those that did perforation corrosion for 499 to 300 cycles were good, and those that did not perforate in less than 300 cycles. Corrosion is indicated by x. The coating blistering corrosion resistance is determined by measuring the swollen width of the coating from the cross-cut portion after 100 cycles of the composite corrosion test according to JIS H8502, and the width is less than 3 mm. Are marked with ◯, and those with 5 mm or more are marked with ×.
In Table 3, No. No. 9 is a butt joint weld of a molten Zn-Al-Mg alloy-plated steel sheet and a GA material. 18 shows the result of butt joint welding of GA materials.
表３に示す結果からもわかるように、Ｎｏ．１〜９，１１〜１３及び１５のように、めっき成分にＡｌが３質量％以上含まれ、かつ片面当りのめっき付着量が２０ｇ／ｍ2以上の場合、溶接時にめっき金属のＡｌが溶融池に混入し、溶融金属の粘性を下げて流動しやすい状態にすることから、後方の溶融金属がキーホールを充填しやすくして、溶接ビードにハンピングや穴開きが発生し難くなっている。
めっき付着量が少なかったり（Ｎｏ．１０）、めっき成分のＡｌ量が少なかったり（Ｎｏ．１４）すると、キーホールの充填が不十分で溶接ビードにハンピングや穴開きが見られた。また、めっき付着量が少なかったり（Ｎｏ．１０）、めっき成分のＭｇ量が少なかったり（Ｎｏ．１２）すると、耐穴あき腐食性が不十分であった。さらに、めっき成分のＡｌ量が多すぎたり（Ｎｏ．１１）、めっき成分のＭｇ量が多すぎたり（Ｎｏ．１３）すると、却って耐塗膜膨れ腐食性が低下している。
As can be seen from the results shown in Table 3, no. As in 1 to 9, 11 to 13 and 15, when the plating component contains 3 mass% or more of Al and the amount of plating deposited on one side is 20 g / m 2 or more, the plating metal Al is molten pool during welding. Therefore, the molten metal at the rear is easy to fill the keyhole, and the welding bead is less likely to be humped or perforated.
When the amount of plating adhered was small (No. 10) or the amount of Al of the plating component was small (No. 14), the keyhole was insufficiently filled and humping or perforation was observed in the weld bead. Further, when the amount of plating adhesion was small (No. 10) or the amount of Mg of the plating component was small (No. 12), the perforated corrosion resistance was insufficient. Furthermore, if the amount of Al of the plating component is too large (No. 11) or the amount of Mg of the plating component is too large (No. 13), the coating film swelling and corrosion resistance is deteriorated.
Claims (2)
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005034937A JP4889224B2 (en) | 2005-02-10 | 2005-02-10 | Method for producing tailored blanks |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005034937A JP4889224B2 (en) | 2005-02-10 | 2005-02-10 | Method for producing tailored blanks |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2006218518A true JP2006218518A (en) | 2006-08-24 |
| JP4889224B2 JP4889224B2 (en) | 2012-03-07 |
Family
ID=36981168
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2005034937A Expired - Lifetime JP4889224B2 (en) | 2005-02-10 | 2005-02-10 | Method for producing tailored blanks |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP4889224B2 (en) |
Cited By (11)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007146199A (en) * | 2005-11-25 | 2007-06-14 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
| JP2008055479A (en) * | 2006-08-31 | 2008-03-13 | Jfe Steel Kk | Metal plate butt joining method and joined metal plate |
| JP2010535636A (en) * | 2007-08-15 | 2010-11-25 | コラス・スタール・ベー・ブイ | Method for producing coated steel strips for producing tailored blanks suitable for thermomechanical forming, strips produced thereby and use of such coated strips |
| JP2011208264A (en) * | 2010-03-30 | 2011-10-20 | Nisshin Steel Co Ltd | Vehicle chassis member excellent in corrosion resistance and method of manufacturing the same |
| JP2012007243A (en) * | 2011-09-27 | 2012-01-12 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
| JP2015510453A (en) * | 2012-12-03 | 2015-04-09 | ヒュンダイ ハイスコ カンパニー リミテッド | Tailored blank, manufacturing method thereof and hot stamping component using the same |
| GB2521363A (en) * | 2013-12-17 | 2015-06-24 | Eaton Ind Netherlands Bv | Method for producing a housing for medium voltage switchgear and such a housing |
| CN109848560A (en) * | 2019-03-18 | 2019-06-07 | 中国科学院上海光学精密机械研究所 | A laser arc composite heat source device and its welding method |
| US10473130B2 (en) | 2006-04-19 | 2019-11-12 | Arcelormittal France | Steel part |
| US10828729B2 (en) | 2011-07-26 | 2020-11-10 | Arcelormittal | Hot-formed previously welded steel part with very high mechanical resistance and production method |
| US20210395856A1 (en) * | 2015-07-30 | 2021-12-23 | Arcelormittal | Painted, hot formed, coated steel part |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1052777A (en) * | 1996-08-07 | 1998-02-24 | Nisshin Steel Co Ltd | Laser beam welding of plated steel sheet and stainless steel sheet |
| JP2000309843A (en) * | 1999-04-23 | 2000-11-07 | Nippon Steel Corp | Tailored blank for press forming excellent in formability and method for producing the same |
| JP2004209513A (en) * | 2002-12-27 | 2004-07-29 | Nippon Steel Corp | Arc welding method for zinc-based alloy coated steel sheet |
| JP2004315848A (en) * | 2003-02-27 | 2004-11-11 | Nisshin Steel Co Ltd | HOT-DIP Zn-Al-Mg COATED STEEL SHEET FREE FROM WELDING CRACK DUE TO LIQUID METAL EMBRITTLEMENT |
-
2005
- 2005-02-10 JP JP2005034937A patent/JP4889224B2/en not_active Expired - Lifetime
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH1052777A (en) * | 1996-08-07 | 1998-02-24 | Nisshin Steel Co Ltd | Laser beam welding of plated steel sheet and stainless steel sheet |
| JP2000309843A (en) * | 1999-04-23 | 2000-11-07 | Nippon Steel Corp | Tailored blank for press forming excellent in formability and method for producing the same |
| JP2004209513A (en) * | 2002-12-27 | 2004-07-29 | Nippon Steel Corp | Arc welding method for zinc-based alloy coated steel sheet |
| JP2004315848A (en) * | 2003-02-27 | 2004-11-11 | Nisshin Steel Co Ltd | HOT-DIP Zn-Al-Mg COATED STEEL SHEET FREE FROM WELDING CRACK DUE TO LIQUID METAL EMBRITTLEMENT |
Cited By (20)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2007146199A (en) * | 2005-11-25 | 2007-06-14 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
| US10473130B2 (en) | 2006-04-19 | 2019-11-12 | Arcelormittal France | Steel part |
| US11154950B2 (en) | 2006-04-19 | 2021-10-26 | Arcelormittal France | Method for creating a welded steel part with uniform microstructure |
| US10626903B2 (en) | 2006-04-19 | 2020-04-21 | Arceloemittal France | Steel part |
| US10626902B2 (en) | 2006-04-19 | 2020-04-21 | Arcelormittal France | Steel part |
| US10480554B2 (en) | 2006-04-19 | 2019-11-19 | Arcelormittal France | Steel part |
| JP2008055479A (en) * | 2006-08-31 | 2008-03-13 | Jfe Steel Kk | Metal plate butt joining method and joined metal plate |
| JP2010535636A (en) * | 2007-08-15 | 2010-11-25 | コラス・スタール・ベー・ブイ | Method for producing coated steel strips for producing tailored blanks suitable for thermomechanical forming, strips produced thereby and use of such coated strips |
| JP2011208264A (en) * | 2010-03-30 | 2011-10-20 | Nisshin Steel Co Ltd | Vehicle chassis member excellent in corrosion resistance and method of manufacturing the same |
| US10919117B2 (en) | 2011-07-26 | 2021-02-16 | ArcelorMittal Investigación y Desarrollo, S.L. | Hot-formed previously welded steel part with very high mechanical resistance and production method |
| US10828729B2 (en) | 2011-07-26 | 2020-11-10 | Arcelormittal | Hot-formed previously welded steel part with very high mechanical resistance and production method |
| US11426820B2 (en) | 2011-07-26 | 2022-08-30 | Arcelormittal | Hot-formed previously welded steel part with very high mechanical resistance and production method |
| JP2012007243A (en) * | 2011-09-27 | 2012-01-12 | Nisshin Steel Co Ltd | Rust-preventive structure for automobile |
| US9884468B2 (en) | 2012-12-03 | 2018-02-06 | Hyundai Steel Company | Tailor welded blank, manufacturing method thereof, and hot stamped component using tailor welded blank |
| US9381720B2 (en) | 2012-12-03 | 2016-07-05 | Hyundai Steel Company | Tailor welded blank, manufacturing method thereof, and hot stamped component using tailor welded blank |
| JP2015510453A (en) * | 2012-12-03 | 2015-04-09 | ヒュンダイ ハイスコ カンパニー リミテッド | Tailored blank, manufacturing method thereof and hot stamping component using the same |
| GB2521363A (en) * | 2013-12-17 | 2015-06-24 | Eaton Ind Netherlands Bv | Method for producing a housing for medium voltage switchgear and such a housing |
| US20210395856A1 (en) * | 2015-07-30 | 2021-12-23 | Arcelormittal | Painted, hot formed, coated steel part |
| US20210395853A1 (en) * | 2015-07-30 | 2021-12-23 | Arcelormittal | Hot formed pre-coated steel part |
| CN109848560A (en) * | 2019-03-18 | 2019-06-07 | 中国科学院上海光学精密机械研究所 | A laser arc composite heat source device and its welding method |
Also Published As
| Publication number | Publication date |
|---|---|
| JP4889224B2 (en) | 2012-03-07 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US10857619B2 (en) | Control of intermetallic compound growth in aluminum to steel resistance welding | |
| JP4519508B2 (en) | Dissimilar joints of steel and aluminum | |
| EP3815837A1 (en) | Different-strength steel welding component with aluminum or aluminum-alloy plating and method for manufacturing same | |
| JP6451327B2 (en) | Overlapping blank for hot stamping, method for manufacturing overlapping hot stamping molded body, and overlapping hot stamping molded body | |
| WO2019245025A1 (en) | Steel plate, tailored blank, hot press-formed product, steel pipe, hollow quenched formed product, and method for manufacturing steel plate | |
| JPWO2006046608A1 (en) | Method of joining iron-based member and aluminum-based member | |
| JP4889224B2 (en) | Method for producing tailored blanks | |
| JP7588181B2 (en) | Welding method for the manufacture of an assembly of at least two metal substrates | |
| US20060289393A1 (en) | Method of TIG braze-welding using an argon/helium/hydrogen mixture | |
| JP4958498B2 (en) | Joint for joining aluminum product and steel product and joining method using the same | |
| US20200016679A1 (en) | Pretreatment of weld flanges to mitigate liquid metal embrittlement cracking in resistance welding of galvanized steels | |
| JP7194269B2 (en) | Assembly of at least two metal substrates | |
| JP2004001085A (en) | Filler metal for welding aluminum alloy and welding method for aluminum alloy using it | |
| JP2008080394A (en) | Joined body of dissimilar materials comprising steel and aluminum and joining method therefor | |
| KR102061470B1 (en) | MIG brazing method, manufacturing method of overlap joint member, and overlap joint member | |
| US11548091B2 (en) | Pretreatment of weld flanges to mitigate liquid metal embrittlement cracking in resistance welding of galvanized steels | |
| JP2006312192A (en) | Method for joining dissimilar metal product | |
| JP3283826B2 (en) | Automotive fuel container with excellent corrosion resistance | |
| JPH08269738A (en) | Zn-Ni alloy plated steel sheet with excellent laser weldability | |
| JP2001355051A (en) | Hot-dip Zn-Sn-based plated steel sheet with excellent corrosion resistance | |
| JP2007146199A (en) | Rust-preventive structure for automobile | |
| JP2002361461A (en) | Superposition laser welding method of galvanized steel sheet with excellent corrosion resistance | |
| JP5389133B2 (en) | Rust-proof structure for automobiles | |
| JP6939826B2 (en) | Al-based galvanized steel sheet and its manufacturing method | |
| Ioannou | Mechanical behaviour and corrosion of interstitial-free steel-aluminium alloy self-piercing riveted joints |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| RD04 | Notification of resignation of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7424 Effective date: 20070313 |
|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20080205 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20100406 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20100511 |
|
| RD02 | Notification of acceptance of power of attorney |
Free format text: JAPANESE INTERMEDIATE CODE: A7422 Effective date: 20100705 |
|
| A02 | Decision of refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A02 Effective date: 20101116 |
|
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20111213 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 4889224 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20141222 Year of fee payment: 3 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| S111 | Request for change of ownership or part of ownership |
Free format text: JAPANESE INTERMEDIATE CODE: R313111 |
|
| R350 | Written notification of registration of transfer |
Free format text: JAPANESE INTERMEDIATE CODE: R350 |