JP2018122307A - Pulsed mag welding method for thin steel sheet - Google Patents
Pulsed mag welding method for thin steel sheet Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 64
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 29
- 239000010959 steel Substances 0.000 title claims abstract description 29
- 238000000034 method Methods 0.000 title claims abstract description 22
- 239000007787 solid Substances 0.000 claims abstract description 7
- 229910052750 molybdenum Inorganic materials 0.000 claims description 11
- 229910052759 nickel Inorganic materials 0.000 claims description 11
- 239000012535 impurity Substances 0.000 claims description 5
- 239000011324 bead Substances 0.000 abstract description 41
- 230000007547 defect Effects 0.000 abstract description 7
- 230000002349 favourable effect Effects 0.000 abstract 2
- 239000002893 slag Substances 0.000 description 29
- 239000010949 copper Substances 0.000 description 15
- 229910052751 metal Inorganic materials 0.000 description 11
- 239000002184 metal Substances 0.000 description 11
- 230000000694 effects Effects 0.000 description 10
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 10
- 229910052802 copper Inorganic materials 0.000 description 6
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 5
- 239000003973 paint Substances 0.000 description 5
- 239000000203 mixture Substances 0.000 description 4
- 238000007747 plating Methods 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 238000005336 cracking Methods 0.000 description 3
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 230000000087 stabilizing effect Effects 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 1
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 description 1
- 230000004931 aggregating effect Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910000423 chromium oxide Inorganic materials 0.000 description 1
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910000480 nickel oxide Inorganic materials 0.000 description 1
- GNRSAWUEBMWBQH-UHFFFAOYSA-N oxonickel Chemical compound [Ni]=O GNRSAWUEBMWBQH-UHFFFAOYSA-N 0.000 description 1
- 230000002265 prevention Effects 0.000 description 1
- 230000001932 seasonal effect Effects 0.000 description 1
- 238000000926 separation method Methods 0.000 description 1
- 229910052814 silicon oxide Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
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- Arc Welding In General (AREA)
Abstract
Description
本発明は、薄鋼板のパルスＭＡＧ溶接方法に関し、特に板厚が１．２〜６ｍｍの薄鋼板の重ね継手部やＴ継手部を溶接するに際してビード表面に残存するスラグがなく、アークを安定させてスパッタ発生量が少なく、ビード形状が良好で、溶接欠陥がないなど、高能率で高品質な溶接部を得る上で好適な薄鋼板のパルスＭＡＧ溶接方法に関する。 The present invention relates to a pulse MAG welding method for a thin steel plate, and in particular, when welding a lap joint portion or a T joint portion of a thin steel plate having a thickness of 1.2 to 6 mm, there is no slag remaining on the bead surface and the arc is stabilized. In particular, the present invention relates to a pulse MAG welding method for a thin steel sheet suitable for obtaining a high-efficiency and high-quality welded part such as a low spatter generation amount, a good bead shape, and no welding defects.
自動車の足回り部材は、板厚が１．２〜６ｍｍの薄鋼板の場合がほとんどで、通常、溶接後に防錆および美観のために塗料を電着塗装される。
自動車用薄鋼板の足回り部材の溶接は、ガスシールドアーク溶接用ソリッドワイヤを用いて継手部の品質特性の面からスパッタの発生量を低減させて部材への付着を少なくする目的と、高速度での溶接性確保の面からシールドガスとしてＡｒガスを主成分とし、これにＣＯ2ガスを混合、さらにはＯ2ガスを混合したガスを用いたパルスＭＡＧ溶接方法が近年増加している。パルスＭＡＧ溶接方法は、平均電流を低くして溶接できることから薄鋼板の溶接では耐溶け落ち性も向上できるとともに、高速度の溶接条件で施工できるので生産性が高く、品質の良好な溶接継手部が得られる。
The undercarriage member of an automobile is mostly a thin steel plate having a thickness of 1.2 to 6 mm, and is usually electrodeposited with a paint for rust prevention and aesthetic appearance after welding.
The purpose of welding undercarriage members of thin steel sheets for automobiles is to reduce the amount of spatter generated by using solid wire for gas shielded arc welding and to reduce the amount of spatter generated from the aspect of quality characteristics of the joints, and at high speed. Ar gas as a main component as the shielding gas from the viewpoint of weldability secure, the mixing CO 2 gas thereto, further the pulse MAG welding method using a mixed gas of O 2 gas is increased in recent years. The pulse MAG welding method can weld with a low average current, so it can improve the melt-off resistance when welding thin steel plates, and it can be applied under high-speed welding conditions, so it is highly productive and has good quality. Is obtained.
パルスＭＡＧ溶接とは、溶接電流として平均電流値より高電流となるピーク電流と平均
電流値より低電流としたベース電流を周期的に流す溶接方法である。これによりピーク電流期間では一定に送給されている溶接用ワイヤを電磁ピンチ力などの作用で溶滴状態に溶融させ、ベース電流期間中にこの溶滴を溶融池に安定的に移行させるので、高速溶接時に溶滴が溶融池と短絡することなくスムーズに溶融池へ移行させることができる。
Pulse MAG welding is a welding method in which a peak current that is higher than the average current value as a welding current and a base current that is lower than the average current value are periodically passed. As a result, the welding wire, which is constantly fed during the peak current period, is melted into a droplet state by an action such as an electromagnetic pinch force, and this droplet is stably transferred to the molten pool during the base current period. The droplets can be smoothly transferred to the molten pool without short-circuiting with the molten pool during high-speed welding.
このように、パルス溶接電源を適用することにより、パルスＭＡＧ溶接においてピーク
電流、ピーク時間、アーク電圧の積からなる溶融エネルギーに対応したワイヤ送給量毎の溶滴生成量にする。すなわち、１回のパルスピーク電流時に１個の溶滴を生成させ、ベース電流期間に溶滴を溶融池に規則的に移行させる１パルス−１ドロップ移行となるパルス条件とするにより、溶滴はスムーズに溶融池に移行してスパッタ発生量が低減される。このため溶接電源は、溶接用ワイヤの送給速度に対応してパルスの周波数を数十Ｈｚ〜３００Ｈｚ程度まで変化させることが可能となっている。
In this way, by applying the pulse welding power source, the droplet generation amount for each wire feeding amount corresponding to the melting energy consisting of the product of peak current, peak time, and arc voltage in pulse MAG welding is obtained. That is, by forming a single droplet at the time of one pulse peak current and setting a pulse condition of 1 pulse-1 drop transition that regularly transfers the droplet to the molten pool during the base current period, The amount of spatter generated is reduced by smoothly moving to the molten pool. For this reason, the welding power source can change the frequency of the pulse from about several tens of Hz to about 300 Hz corresponding to the feeding speed of the welding wire.
薄鋼板溶接のパルスＭＡＧ溶接用ワイヤとして、例えば、特開平８−９９１７５号公報
（特許文献１）に、薄板高張力鋼板をワイヤ成分、シールドガス組成およびパルス付与条件を限定して溶接し、溶接金属の機械的性質を良好にすることができるとともにスパッタの発生量が少なく溶接作業性に優れる技術が開示されている。しかし、特許文献１に開示の技術においても、アークが安定して、ビード形状が良好な溶接金属を得ることができない。さらに、スラグ生成量が多くなり塗料を塗装後にスラグとともに塗料が剥がれるという問題があった。
As a pulse MAG welding wire for thin steel plate welding, for example, in Japanese Patent Application Laid-Open No. Hei 8-99175 (Patent Document 1), a thin high strength steel plate is welded by limiting the wire component, shield gas composition and pulse application conditions, and welding. A technique that can improve the mechanical properties of a metal and that has a low spatter generation amount and excellent welding workability is disclosed. However, even with the technique disclosed in Patent Document 1, it is impossible to obtain a weld metal with a stable arc and a good bead shape. Furthermore, there was a problem that the amount of slag generation increased and the paint was peeled off together with the slag after the paint was applied.
また、特開平９−２３９５８３号公報（特許文献２）、特開２００１−３２１９８５号
公報（特許文献３）および特開２００９−１６６０６６号公報（特許文献４）には、パルスＭＡＧ溶接用ソリッドワイヤの開示がある。しかし、特許文献２〜特許文献４に記載の溶接用ソリッドワイヤを用いたパルスＭＡＧ溶接においても、スラグ生成量が多く塗装後にスラグとともに塗料が剥がれるという問題があった。
In addition, Japanese Patent Laid-Open No. 9-239583 (Patent Document 2), Japanese Patent Laid-Open No. 2001-321985 (Patent Document 3) and Japanese Patent Laid-Open No. 2009-166066 (Patent Document 4) describe a solid wire for pulse MAG welding. There is disclosure. However, even in the pulse MAG welding using the welding solid wire described in Patent Documents 2 to 4, there is a problem that the amount of slag generated is large and the paint is peeled off together with the slag after coating.
一方、特開２０１６−２０３２４７号公報（特許文献５）には、ガスシールドアーク溶
接用フラックス入りワイヤにシリコン酸化物、クロム酸化物およびニッケル酸化物の少なくとも１種を含有させて薄鋼板の溶接をし、ビード表面に酸化皮膜層を形成して塗料塗装後の剥離を防止した技術の開示がある。しかし、特許文献５に開示されているビード表面の酸化皮膜層は、自動車の車体構造部材に適用した場合、季節の変化、寒冷地および温暖地など自動車の使用環境の温度差による溶接金属と酸化皮膜層との熱膨張の差によって酸化皮膜層が塗料とともに剥がれるという問題がある。
On the other hand, in JP-A-2006-203247 (Patent Document 5), welding of thin steel sheets is performed by containing at least one of silicon oxide, chromium oxide and nickel oxide in a flux-cored wire for gas shield arc welding. In addition, there is a disclosure of a technique in which an oxide film layer is formed on the bead surface to prevent peeling after coating. However, when the bead surface oxide film layer disclosed in Patent Document 5 is applied to a body structure member of an automobile, it is oxidized with a weld metal due to a temperature difference in an environment in which the automobile is used, such as seasonal changes, cold regions and warm regions. There is a problem that the oxide film layer is peeled off together with the paint due to a difference in thermal expansion from the film layer.
そこで本発明は、上述した問題点に鑑みて案出されたものであり、板厚が１．２〜６ｍ
ｍである薄鋼板の重ね継手部やＴ継手部を溶接するに際してビード表面に残存するスラグがなく、アークが安定してスパッタ発生量が少なく、ビード形状が良好で溶接欠陥がないなど、高能率に高品質な溶接部が得られる薄鋼板のパルスＭＡＧ溶接方法を提供することを目的とする。
Therefore, the present invention has been devised in view of the above-described problems, and has a thickness of 1.2 to 6 m.
High efficiency, such as no slag remaining on the bead surface when welding lap joints and T joints of thin steel plates of m, stable arc, low spatter generation, good bead shape and no weld defects Another object of the present invention is to provide a pulse MAG welding method for a thin steel plate that can obtain a high-quality weld.
本発明の要旨は、板厚１．２〜６ｍｍである薄鋼板のパルスＭＡＧ溶接方法において、
ワイヤ全質量に対する質量％で、Ｃ：０．００５〜０．０８％、Ｓｉ：０．２０〜０．５０％、Ｍｎ：１．００〜１．６０％、Ｓｂ：０．０２〜０．２０％、Ｃｕ：０．０８〜０．４５％を含有し、Ｐ：０．０２％以下、Ｓ：０．０２％以下であり、残部はＦｅおよび不可避不純物よりなるソリッドワイヤを用いて、パルスピーク電流（Ｉｐ）：４４０〜６００Ａ、パルスベース電流（Ｉｂ）：３０〜８０Ａとし、前記パルスピーク電流（Ｉｐ）とパルスピーク時間（Ｔｐ）が下記式（１）を満足するパルスを付加して溶接することを特徴とする薄鋼板のパルスＭＡＧ溶接方法。
４１５≦Ｉｐ（Ａ）×Ｔｐ（ｍｓｅｃ）≦７８０・・・・・（１）
The gist of the present invention is a pulse MAG welding method of a thin steel plate having a thickness of 1.2 to 6 mm.
% By mass with respect to the total mass of the wire, C: 0.005 to 0.08%, Si: 0.20 to 0.50%, Mn: 1.00 to 1.60%, Sb: 0.02 to 0.20 %, Cu: 0.08 to 0.45%, P: 0.02% or less, S: 0.02% or less, and the balance is a pulse peak using a solid wire made of Fe and inevitable impurities. Current (Ip): 440 to 600 A, pulse base current (Ib): 30 to 80 A, a pulse in which the pulse peak current (Ip) and the pulse peak time (Tp) satisfy the following formula (1) is added and welding is performed. A pulse MAG welding method for a thin steel sheet.
415 ≦ Ip (A) × Tp (msec) ≦ 780 (1)
また、ワイヤ全質量に対する質量％で、ＮｉおよびＭｏの１種または２種の合計：０．
４０％以下をさらに含有することも特徴とする薄鋼板のパルスＭＡＧ溶接方法にある。
Moreover, it is the mass% with respect to the total mass of the wire, and the total of one or two of Ni and Mo: 0.0.
The pulse MAG welding method of a thin steel sheet is characterized by further containing 40% or less.
本発明の薄鋼板のパルスＭＡＧ溶接方法によれば、板厚が１．２〜６ｍｍの薄鋼板の重
ね継手部やＴ継手部を溶接するに際してビード表面に残存するスラグがなく、アークが安定してスパッタ発生量が少なく、ビード形状が良好で溶接欠陥がないなど、高能率に高品質な溶接部が得られる。
According to the pulse MAG welding method of a thin steel plate of the present invention, when welding a lap joint portion or a T joint portion of a thin steel plate having a thickness of 1.2 to 6 mm, there is no slag remaining on the bead surface, and the arc is stabilized. As a result, the spatter generation amount is small, the bead shape is good and there are no welding defects, and a high-quality welded portion can be obtained with high efficiency.
本発明者らは、上述した問題点を解決するために、薄鋼板を重ねすみ肉継手とし、各種成分のソリッドワイヤを用いて各種パルス条件で０．８ｍ／ｍｉｎ以上の溶接速度で溶接を行い、ビード表面に残存するスラグの有無、アークの安定性、スパッタの発生状況、ビード形状および溶接欠陥の有無について詳細に検討した結果、次の知見を得た。 In order to solve the above-mentioned problems, the present inventors made thin steel plates into a fillet joint, and welded at a welding speed of 0.8 m / min or more under various pulse conditions using solid wires of various components. As a result of detailed examination of the presence or absence of slag remaining on the bead surface, the stability of the arc, the occurrence of spatter, the bead shape and the presence or absence of welding defects, the following knowledge was obtained.
（１）ワイヤ組成は、Ｓｉの含有量およびＭｎの含有量を適正としてスラグ生成量を少なくし、Ｓｂの含有量を適正化することによって、少量生成したスラグを溶融プール表面に浮上することができ、溶融プールに浮上したスラグをクレータ部まで運ぶことによってビード表面に残存するスラグがなくなるという効果が得られた。また、Ｃの含有量、Ｍｎの含有量、Ｓｉの含有量およびＣｕの含有量の適正化によって、アークが安定してスパッタ発生量の少ない溶接ができた。さらに、ＮｉおよびＭｏを適量含有することによって、生成スラグが溶融プール表面に浮上したままクレータ部まで移動する効果を向上することができた。 (1) The wire composition may cause a small amount of slag to float on the surface of the molten pool by optimizing the Sb content by reducing the slag generation amount with the appropriate Si content and Mn content. It was possible to obtain the effect that the slag remaining on the bead surface disappeared by transporting the slag that floated to the molten pool to the crater portion. Further, by optimizing the C content, the Mn content, the Si content, and the Cu content, the arc was stabilized and welding with less spatter generation was achieved. Furthermore, by containing appropriate amounts of Ni and Mo, the effect of moving the generated slag to the crater portion while floating on the molten pool surface could be improved.
（２）上述した組成のワイヤを用いてパルス条件が１パルス−１ドロップの溶滴移行となる領域にすることで、８０ｃｍ／ｍｉｎ以上の高速度の溶接でアークが安定してスパッタ発生量が少なく良好なビード形状が得られる。 (2) By using the wire having the above-described composition and making the region where the pulse condition is 1 pulse-1 drop droplet transfer, the arc is stabilized by high-speed welding at 80 cm / min or more, and the amount of spatter generated is reduced. Less bead shape can be obtained.
以下、本発明の薄鋼板のパルスＭＡＧ溶接方法の限定理由について説明する。
まず、ワイヤ成分組成について説明する。なお、各成分の含有率は、ワイヤ全質量に対する質量％で表すものとし、その質量％に関する記載を単に％と記載する。
Hereinafter, the reason for limitation of the pulse MAG welding method of the thin steel plate of this invention is demonstrated.
First, the wire component composition will be described. In addition, the content rate of each component shall be represented by the mass% with respect to the total mass of a wire, and the description regarding the mass% is only described as%.
［Ｃ：０．００５〜０．０８％］
Ｃは、アークを安定させて溶滴を細粒化する作用がある。Ｃが０．００５％未満では、溶滴の細粒化が困難となってアークが不安定でスパッタ発生量が多くなる。一方、Ｃが０．０８％を超えると、スパッタ発生量が多くなるばかりでなく、溶接金属の耐割れ性が劣化する。したがって、Ｃは０．００５〜０．０８％とする。
[C: 0.005 to 0.08%]
C has the effect of stabilizing the arc and making the droplets fine. If C is less than 0.005%, it is difficult to make the droplets finer, the arc becomes unstable, and the amount of spatter generated increases. On the other hand, if C exceeds 0.08%, not only the amount of spatter generated increases, but also the crack resistance of the weld metal deteriorates. Therefore, C is 0.005 to 0.08%.
［Ｓｉ：０．２０〜０．５０％］
Ｓｉは、溶融金属の表面張力を調整してビード形状を良好にする作用がある。Ｓｉが０．２０％未満では、上記効果が得られず、ビード形状が不良となる。一方、Ｓｉが０．５０％を超えると、溶融金属の表面張力が過度に上昇するため凸ビードとなりやすい。また、アークが不安定でスパッタ発生量、スラグ生成量が多くなる。したがって、Ｓｉは０．２０〜０．５０％とする。
[Si: 0.20 to 0.50%]
Si has the effect of adjusting the surface tension of the molten metal to improve the bead shape. If Si is less than 0.20%, the above effect cannot be obtained, and the bead shape becomes poor. On the other hand, when the Si content exceeds 0.50%, the surface tension of the molten metal is excessively increased, so that a convex bead tends to be formed. Further, the arc is unstable, and the amount of spatter generation and slag generation increases. Therefore, Si is 0.20 to 0.50%.
［Ｍｎ：１．００〜１．６０％］
Ｍｎは、脱酸元素として重要な元素である。Ｍｎが１．００％未満では、特に高速度の溶接条件でピットが発生しやすくなる。一方、Ｍｎが１．６０％を超えると、スパッタ発生量およびスラグ生成量が多くなる。したがって、Ｍｎは１．００〜１．６０％とする。
[Mn: 1.00 to 1.60%]
Mn is an important element as a deoxidizing element. If Mn is less than 1.00%, pits are likely to be generated particularly under high-speed welding conditions. On the other hand, when Mn exceeds 1.60%, the amount of spatter generation and the amount of slag generation increase. Therefore, Mn is set to 1.00 to 1.60%.
［Ｓｂ：０．０２〜０．２０％］
Ｓｂは、溶接時に生成した少量のスラグを溶融プール表面に浮上させてクレータ部まで運ぶことによってビード表面に残存するスラグを無くす効果がある。Ｓｂが０．０２％未満であると、生成したスラグを溶融プール表面に浮上させてクレータ部まで運ぶ効果が少なくなりスラグがビード表面に残存する。一方、Ｓｂが０．２０％を超えると、溶接金属の耐割れ性が劣化する。したがって、Ｓｂは０．０２〜０．２０％とする。
[Sb: 0.02 to 0.20%]
Sb has the effect of eliminating slag remaining on the bead surface by floating a small amount of slag generated during welding to the surface of the molten pool and carrying it to the crater portion. When Sb is less than 0.02%, the effect of floating the generated slag on the surface of the molten pool and transporting it to the crater portion is reduced, and the slag remains on the bead surface. On the other hand, if Sb exceeds 0.20%, the crack resistance of the weld metal deteriorates. Therefore, Sb is set to 0.02 to 0.20%.
［Ｃｕ：０．０８〜０．４５％］
Ｃｕは、鋼中に不可避的不純物として０．０２％程度含有されるが、本発明のＣｕは主としてワイヤ表面に施した銅めっきをいう。通常、銅めっきはワイヤ送給性と通電性を安定化するのに極めて重要な表面処理方法である。銅めっき厚が薄いと溶接中のチップ磨耗が激しくなり、溶接中にワイヤ送給性と通電性が劣化し、その結果、アークが不安定になる。Ｃｕが０．０８％未満であると、必要なワイヤ送給性と通電性が得られずアークが不安定となる。一方、Ｃｕが０．４５％を超えると、溶接金属の耐割れ性が劣化する。したがって、Ｃｕは０．０８〜０．４５％とする。なお、ワイヤ表面の銅めっき厚さは０．２〜１．０μｍであることが耐チップ磨耗性および通電性から好ましい。
[Cu: 0.08 to 0.45%]
Cu is contained in steel in an amount of about 0.02% as an inevitable impurity, but Cu of the present invention mainly refers to copper plating applied to the wire surface. In general, copper plating is a surface treatment method that is extremely important for stabilizing the wire feeding property and the current carrying property. If the copper plating thickness is thin, tip wear during welding becomes severe, and wire feedability and electrical conductivity deteriorate during welding, resulting in an unstable arc. If the Cu content is less than 0.08%, the required wire feedability and electrical conductivity cannot be obtained and the arc becomes unstable. On the other hand, if Cu exceeds 0.45%, the crack resistance of the weld metal deteriorates. Therefore, Cu is made 0.08 to 0.45%. In addition, it is preferable that the copper plating thickness of the wire surface is 0.2-1.0 micrometer from chip | tip wear resistance and electrical conductivity.
［Ｐ：０．０２％以下］
Ｐは不純物であり、Ｐの増加により溶接金属の割れを引き起こすので０．０２％以下とする。好ましくは０．０１５％以下である。
［Ｓ：０．０２％以下］
Ｓは不純物であり、Ｓの増加により溶接金属の割れを引き起こすので０．０２％以下とする。好ましくは０．０１５％以下である。
[P: 0.02% or less]
P is an impurity, and an increase in P causes cracks in the weld metal. Preferably it is 0.015% or less.
[S: 0.02% or less]
S is an impurity, and an increase in S causes cracking of the weld metal, so 0.02% or less. Preferably it is 0.015% or less.
［ＮｉおよびＭｏの１種または２種の合計：０．４０％以下］
ＮｉおよびＭｏは、Ｓｂの生成スラグの溶融プールへ浮上させる作用を助長する。すなわち、ＮｉおよびＭｏは、溶融プールを小さくし、生成した少量のスラグをアーク点近傍の溶融プール上に凝集させてクレータ部まで移動する作用を有する。ＮｉおよびＭｏの１種または２種の合計が０．４０％を超えると、溶接金属の耐割れ性が劣化する。したがって、ＮｉおよびＭｏの１種または２種の合計は０．４０％以下とする。なお、前記効果を得るためのＮｉおよびＭｏの１種または２種の合計は０．０５％以上である。
[Total of one or two of Ni and Mo: 0.40% or less]
Ni and Mo promote the action of levitating the generated slag of Sb to the molten pool. That is, Ni and Mo have a function of making the molten pool small and aggregating a small amount of generated slag on the molten pool near the arc point to move to the crater portion. If the total of one or two of Ni and Mo exceeds 0.40%, the crack resistance of the weld metal deteriorates. Therefore, the total of one or two of Ni and Mo is 0.40% or less. The total of one or two of Ni and Mo for obtaining the above effect is 0.05% or more.
さらに、８０ｃｍ／ｍｉｎ以上の高速度の溶接条件でアークが安定してスパッタ発生量が少なく、ビード形状が良好となる最適パルスＭＡＧ条件範囲を検討した結果、１パルス−１ドロップ領域であるパルスピーク電流Ｉｐとパルスピーク時間Ｔｐの領域において、短絡がし難くアークが安定してスパッタ発生量の少ない溶接となり、良好なビード形状が得られる最適のパルスＭＡＧ条件範囲を見出した。 Furthermore, as a result of examining the optimum pulse MAG condition range in which the arc is stable under the high-speed welding conditions of 80 cm / min or more, the amount of spatter generation is small, and the bead shape is good, the pulse peak which is one pulse-1 drop region In the region of the current Ip and the pulse peak time Tp, the optimum pulse MAG condition range in which a short-circuit is difficult to occur, the arc is stable, the amount of spatter generation is small, and a good bead shape is obtained was found.
［パルスピーク電流（Ｉｐ）：４４０〜６００Ａ］
パルスピーク電流（Ｉｐ）が４４０Ａ未満では、電磁ピンチ効果による溶滴の生成と離脱がスムーズに行われなくなり、不均一な凸ビードとなる。また、アークが不安定でスパッタ発生量が多くなる。一方、パルスピーク電流（Ｉｐ）が６００Ａを超えると、アーク力によりスパッタ発生量が多くなる。したがって、パルスピーク電流（Ｉｐ）は４４０〜６００Ａとする。
[Pulse peak current (Ip): 440 to 600 A]
When the pulse peak current (Ip) is less than 440 A, the generation and separation of droplets due to the electromagnetic pinch effect are not smoothly performed, resulting in uneven convex beads. Also, the arc is unstable and the amount of spatter generated increases. On the other hand, when the pulse peak current (Ip) exceeds 600 A, the amount of spatter generated increases due to the arc force. Therefore, the pulse peak current (Ip) is set to 440 to 600A.
［パルスベース電流（Ｉｂ）：３０〜８０Ａ］
パルスベース電流（Ｉｂ）は、ベース期間でアークを保持できる電流値が必要となる。パルスベース電流（Ｉｂ）が３０Ａ未満では、アークが不安定となりスパッタ発生量が多く、ビード形状が劣化する。一方、パルスベース電流（Ｉｂ）が８０Ａを超えると、溶滴の離脱が速やかに行われず、アークが不安定でスパッタ発生量が多くなる。したがって、パルスベース電流（Ｉｂ）は３０〜８０Ａとする。
[Pulse base current (Ib): 30-80A]
The pulse base current (Ib) requires a current value that can hold the arc in the base period. If the pulse base current (Ib) is less than 30 A, the arc becomes unstable, the amount of spatter generated is large, and the bead shape deteriorates. On the other hand, when the pulse base current (Ib) exceeds 80 A, the droplets are not released quickly, the arc is unstable, and the amount of spatter generated increases. Therefore, the pulse base current (Ib) is 30 to 80A.
［４１５≦Ｉｐ（Ａ）×Ｔｐ（ｍｓｅｃ）≦７８０］
下記式（１）で示すパルス電流（Ｉｐ）とパルスピーク時間（Ｔｐ）の積（Ｉｐ×Ｔｐ
）で得られる値を限定することによって、ピーク時間の短い領域でアーク電圧が高い場合においても、溶滴の短絡がピーク時及びベース時に適度に生じて良好なビード形状が得られる。パルスピーク電流（Ｉｐ）とパルスピーク時間（Ｔｐ）の積（Ｉｐ×Ｔｐ）が４１５未満では、ピーク電流期間で溶滴を形成するためのエネルギーが不足し十分な溶滴の形成ができず、凸ビードとなる。一方、パルスピーク電流（Ｉｐ）とパルスピーク時間（Ｔｐ）の積が７８０を超えると、過度に成長した溶滴が短絡しやすくなり再点弧時のアーク力で溶融地が吹き飛ばされることからアークが不安定でスパッタ発生量が多くなる。したがって、Ｉｐ×Ｔｐは、下記式（１）で示される範囲とする。
４１５≦Ｉｐ（Ａ）×Ｔｐ（ｍｓｅｃ）≦７８０ ・・・・（１）
[415 ≦ Ip (A) × Tp (msec) ≦ 780]
The product of the pulse current (Ip) and the pulse peak time (Tp) represented by the following formula (1) (Ip × Tp
By limiting the value obtained in (1), even when the arc voltage is high in a region where the peak time is short, short-circuiting of the droplets occurs moderately at the peak and at the base, and a good bead shape is obtained. If the product (Ip × Tp) of the pulse peak current (Ip) and the pulse peak time (Tp) is less than 415, the energy for forming the droplet is insufficient during the peak current period, and sufficient droplet formation is not possible. It becomes a convex bead. On the other hand, if the product of the pulse peak current (Ip) and the pulse peak time (Tp) exceeds 780, the excessively grown droplets are likely to be short-circuited, and the molten ground is blown away by the arc force at the time of re-ignition. Is unstable and the amount of spatter is increased. Therefore, Ip × Tp is set to a range represented by the following formula (1).
415 ≦ Ip (A) × Tp (msec) ≦ 780 (1)
以下、実施例により本発明の効果をさらに具体的に説明する。
まず、原料鋼を真空溶解し、鍛造、圧延、伸線、焼鈍そして銅めっきした後、１．２ｍ
ｍのワイヤ径まで伸線してスプールに巻き取った試作ワイヤの化学成分を表１に示す。
Hereinafter, the effects of the present invention will be described more specifically with reference to examples.
First, the raw steel is vacuum melted, forged, rolled, drawn, annealed and copper plated, then 1.2m
Table 1 shows chemical components of the prototype wire drawn to a wire diameter of m and wound on a spool.
表１に示す試作ワイヤを用いて、表２に示す板厚３．２ｍｍの鋼板を図１に示す上板１
の端部と下板２の表面との間を、表３および表４に示すパルスＭＡＧ溶接条件で溶接長４００ｍｍを溶接した。ワイヤの狙い位置は重ね継手のコーナー部とし、溶接トーチ２の角度θは６０°とした。溶接試験は、ビード表面のスラグ残存の有無（クレータ部のスラグ
は除く）、アークの安定性、スパッタ発生量、ビード形状および溶接欠陥の有無を目視
で評価した。それらの結果を表４にまとめて示す。
Using the prototype wire shown in Table 1, a steel plate having a thickness of 3.2 mm shown in Table 2 is converted into an upper plate 1 shown in FIG.
A weld length of 400 mm was welded between the end of the plate and the surface of the lower plate 2 under the pulse MAG welding conditions shown in Tables 3 and 4. The target position of the wire was the corner portion of the lap joint, and the angle θ of the welding torch 2 was 60 °. In the welding test, the presence or absence of slag remaining on the bead surface (excluding slag on the crater), the stability of the arc, the amount of spatter, the bead shape, and the presence or absence of welding defects were evaluated visually. The results are summarized in Table 4.
る。
本発明例である試験Ｎｏ．１〜Ｎｏ．８は、ワイヤ記号Ｗ１〜Ｗ８が本発明で規定した各成分範囲内で、パルスＭＡＧ溶接条件が適正であるので、ビード表面へスラグの残存がなく、アークが安定してスパッタ発生量が少なく、ビード形状が良好で溶接欠陥が無く、極めて満足な結果であった。なお、試験Ｎｏ．１、Ｎｏ．４、Ｎｏ．７および試験Ｎｏ．８は、ワイヤ記号Ｗ１、Ｗ４、Ｗ７およびワイヤ記号Ｗ８のＳｉとＭｎの合計が比較的多いのでスラグ生成量も比較的多くなったが、ＮｉおよびＭｏの1種または２種を適量含んでいるので、ビード表面へスラグの残存はなかった。 Test No. which is an example of the present invention. 1-No. No. 8, since the wire symbols W1 to W8 are within the respective component ranges defined in the present invention and the pulse MAG welding conditions are appropriate, no slag remains on the bead surface, the arc is stable, and the amount of spatter generated is small. The bead shape was good, there were no weld defects, and the results were extremely satisfactory. In addition, Test No. 1, no. 4, no. 7 and test no. No. 8 has a relatively large sum of Si and Mn of the wire symbols W1, W4, W7 and the wire symbol W8, so the amount of slag generation was also relatively large, but it contains an appropriate amount of one or two of Ni and Mo. Therefore, no slag remained on the bead surface.
比較例中の試験Ｎｏ．９は、ワイヤ記号Ｗ９のＣが少ないので、アークが不安定でスパ
ッタ発生量が多かった。また、ＮｉとＭｏの合計が多いので、クレータ割れが生じた。
試験Ｎｏ．１０は、ワイヤ記号Ｗ１０のＣが多いので、スパッタ発生量が多く、クレータ割れが発生した。また、パルスピーク電流Ｉｐとピーク時間Ｔｐの積Ｉｐ×Ｔｐが低いので、凸ビードとなった。
Test No. in the comparative example. In No. 9, since the C of the wire symbol W9 is small, the arc is unstable and the amount of spatter generated is large. Moreover, since there was much sum of Ni and Mo, the crater crack occurred.
Test No. No. 10 had a lot of C in the wire symbol W10, so the amount of spatter was large and crater cracking occurred. Further, since the product Ip × Tp of the pulse peak current Ip and the peak time Tp was low, a convex bead was formed.
試験Ｎｏ．１１は、ワイヤ記号Ｗ１１のＳｉが少ないので、ビード形状が不良であった
。また、パルスピーク電流Ｉｐとピーク時間Ｔｐの積Ｉｐ×Ｔｐが高いので、アークが不安定でスパッタ発生量が多かった。試験Ｎｏ．１２は、ワイヤ記号Ｗ１２のＳｉが多いので、ビード表面にスラグが残存し、アークが不安定でスパッタ発生量多く、凸ビードとなった。また、Ｃｕ多いので、クレータ割れが発生した。試験Ｎｏ．１３は、ワイヤ記号Ｗ１３のＭｎが少ないので、ピットが生じた。また、パルスピーク電流（Ｉｐ）が低いので、アークが不安定でスパッタ発生量が多く、凸ビードとなった。
Test No. No. 11 had a poor bead shape because there was less Si in the wire symbol W11. Further, since the product Ip × Tp of the pulse peak current Ip and the peak time Tp is high, the arc is unstable and the amount of spatter generated is large. Test No. No. 12 had a large amount of Si of the wire symbol W12, so slag remained on the bead surface, the arc was unstable, the amount of spatter was large, and a convex bead was formed. Moreover, since there was much Cu, the crater crack generate | occur | produced. Test No. No. 13 had pits because the Mn of the wire symbol W13 was small. Further, since the pulse peak current (Ip) was low, the arc was unstable, the amount of spatter was large, and a convex bead was formed.
試験Ｎｏ．１４は、ワイヤ記号Ｗ１４のＭｎが多いので、ビード表面にスラグが残存し、スパッタ発生量が多かった。試験Ｎｏ．１５は、ワイヤ記号Ｗ１５のＳｂが少ないので、ビード表面にスラグが残存した。また、パルスベース電流（Ｉｂ）が低いので、アークが不安定でスパッタ発生量が多く、ビード形状も不良であった。試験Ｎｏ．１６は、ワイ
ヤ記号Ｗ１６のＳｂが多いので、クレータ割れが発生した。また、パルスベース電流（
Ｉｂ）が高いので、アークが不安定でスパッタ発生量が多かった。
Test No. No. 14 had a large amount of Mn of the wire symbol W14, so that slag remained on the bead surface and the amount of spatter was large. Test No. No. 15 had a small amount of Sb of the wire symbol W15, so that slag remained on the bead surface. Further, since the pulse base current (Ib) was low, the arc was unstable, the amount of spatter generation was large, and the bead shape was poor. Test No. In No. 16, crater cracking occurred because there was much Sb of the wire symbol W16. Also, the pulse base current (
Since Ib) was high, the arc was unstable and the amount of spatter generated was large.
試験Ｎｏ．１７は、ワイヤ記号Ｗ１７のＣｕが少ないので、アークが不安定であった。
また、パルスピーク電流（Ｉｐ）が高いので、スパッタ発生量が多かった。試験Ｎｏ．１
８は、ワイヤ記号Ｗ６が本発明で規定した各成分範囲内であるが、パルスピーク電流Ｉ
ｐとピーク時間Ｔｐの積Ｉｐ×Ｔｐが低いので、凸ビードとなった。試験Ｎｏ．１９は、
ワイヤ記号Ｗ７が本発明で規定した各成分範囲内であるが、パルスピーク電流Ｉｐとピ
ーク時間Ｔｐの積Ｉｐ×Ｔｐが高いので、アークが不安定でスパッタ発生量が多かった。
Test No. In No. 17, the arc of the arc was unstable because there was little Cu in the wire symbol W17.
Further, since the pulse peak current (Ip) was high, the amount of spatter generated was large. Test No. 1
8 is within each component range defined by the wire symbol W6 in the present invention, but the pulse peak current I
Since the product Ip × Tp of p and peak time Tp was low, a convex bead was formed. Test No. 19
Although the wire symbol W7 is within each component range defined in the present invention, the product Ip × Tp of the pulse peak current Ip and the peak time Tp is high, so the arc is unstable and the amount of spatter generated is large.
１ 上板
２ 下板
３ 溶接トーチ
θ トーチ角度
特許出願人 日鐡住金溶接工業株式会社
代理人 弁理士 椎 名 彊
1 Upper plate 2 Lower plate 3 Welding torch θ Torch angle
Patent Applicant Nippon Steel & Sumikin Welding Industry Co., Ltd.
Attorney: Attorney Shiina
Claims (2)
ワイヤ全質量に対する質量％で、
Ｃ：０．００５〜０．０８％、
Ｓｉ：０．２０〜０．５０％、
Ｍｎ：１．００〜１．６０％、
Ｓｂ：０．０２〜０．２０％
Ｃｕ：０．０８〜０．４５％を含有し、
Ｐ：０．０２％以下、
Ｓ：０．０２％以下であり、
残部はＦｅおよび不可避不純物よりなるソリッドワイヤを用いて、
パルスピーク電流（Ｉｐ）：４４０〜６００Ａ、
パルスベース電流（Ｉｂ）：３０〜８０Ａとし、
前記パルスピーク電流（Ｉｐ）とパルスピーク時間（Ｔｐ）が下記式（１）を満足するパルスを付加して溶接することを特徴とする薄鋼板のパルスＭＡＧ溶接方法。
４１５≦Ｉｐ（Ａ）×Ｔｐ（ｍｓｅｃ）≦７８０・・・・・（１） In the pulse MAG welding method of a thin steel plate having a plate thickness of 1.2 to 6 mm,
% By mass relative to the total mass of the wire
C: 0.005-0.08%,
Si: 0.20 to 0.50%,
Mn: 1.00 to 1.60%,
Sb: 0.02 to 0.20%
Cu: 0.08 to 0.45% is contained,
P: 0.02% or less,
S: 0.02% or less,
The remainder uses a solid wire made of Fe and inevitable impurities,
Pulse peak current (Ip): 440 to 600 A,
Pulse base current (Ib): 30-80A,
A pulse MAG welding method for a thin steel sheet, wherein the pulse peak current (Ip) and the pulse peak time (Tp) are welded by applying a pulse satisfying the following formula (1).
415 ≦ Ip (A) × Tp (msec) ≦ 780 (1)
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| CN113500275A (en) * | 2021-07-22 | 2021-10-15 | 南京航空航天大学 | GMAW (gas metal arc welding) welding process for improving formation and performance of high-speed electric arc lap welding seam of sheet steel |
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| JP2004090045A (en) * | 2002-08-30 | 2004-03-25 | Nippon Steel Corp | Gas shielded arc welding wire for low alloy steel excellent in hydrochloric acid resistance and sulfuric acid resistance, and gas shielded arc welding method using same |
| JP2007301623A (en) * | 2006-05-15 | 2007-11-22 | Nippon Steel & Sumikin Welding Co Ltd | High speed gas shielded arc welding method for horizontal lap joint of steel sheet |
| JP2008207211A (en) * | 2007-02-26 | 2008-09-11 | Nippon Steel & Sumikin Welding Co Ltd | Copper-plated solid wire for pulse mag welding |
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| CN113500275A (en) * | 2021-07-22 | 2021-10-15 | 南京航空航天大学 | GMAW (gas metal arc welding) welding process for improving formation and performance of high-speed electric arc lap welding seam of sheet steel |
| CN113500275B (en) * | 2021-07-22 | 2022-06-21 | 南京航空航天大学 | GMAW (gas metal arc welding) welding process for improving formation and performance of high-speed electric arc lap welding seam of sheet steel |
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