JP2857329B2 - Gas shielded arc welding method - Google Patents
Gas shielded arc welding methodInfo
- Publication number
- JP2857329B2 JP2857329B2 JP19061794A JP19061794A JP2857329B2 JP 2857329 B2 JP2857329 B2 JP 2857329B2 JP 19061794 A JP19061794 A JP 19061794A JP 19061794 A JP19061794 A JP 19061794A JP 2857329 B2 JP2857329 B2 JP 2857329B2
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- weight
- wire
- shielded arc
- welding method
- arc welding
- 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.)
- Expired - Lifetime
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- Arc Welding In General (AREA)
- Butt Welding And Welding Of Specific Article (AREA)
- Nonmetallic Welding Materials (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は鋼構造物を横向きで溶接
する横向片面ガスシールドアーク溶接法に関し、特に高
能率横向片面マグ溶接方法に関するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a horizontal one-sided gas shielded arc welding method for welding steel structures in a horizontal direction, and more particularly to a high-efficiency horizontal single-sided MAG welding method.
【０００２】[0002]
【従来の技術】従来の横向片面ガスシールドアーク溶接
においては、基本的な施行条件は以下のとおりである。 開先ルート部に通常約５ｍｍの間隙を設ける。 主として直径１．２ｍｍのワイヤを使用する。 初層の裏波溶接は、通常、溶接電流が２００Ａ、溶接
速度が１０ｃｍ／分というように、低電流且つ低速度で
行う。 ２層目以降は約２８０Ａの中電流で溶接する。2. Description of the Related Art In conventional horizontal one-sided gas shielded arc welding, basic conditions for performing the welding are as follows. There is usually a gap of about 5 mm at the groove root. A wire having a diameter of 1.2 mm is mainly used. Uranami welding of the first layer is usually performed at a low current and a low speed such as a welding current of 200 A and a welding speed of 10 cm / min. The second and subsequent layers are welded with a medium current of about 280A.
【０００３】[0003]
【発明が解決しようとする課題】しかし、この溶接法で
は、以下に示すような問題点がある。 開先ルート部に間隙を設けるため、開先断面積が大き
い。 直径が１．２ｍｍのワイヤを低電流且つ低速度又は中
電流で使用するため、高溶着量を得にくい。 実際の溶接現場では開先ルート部の間隔が変動しやす
く、この開先ルート間隔が縮小した場合には、溶接割れ
が発生しやすい。However, this welding method has the following problems. Since a gap is provided in the groove root portion, the groove cross-sectional area is large. Since a wire having a diameter of 1.2 mm is used at a low current and a low speed or a medium current, it is difficult to obtain a high welding amount. At the actual welding site, the interval between the groove routes is apt to fluctuate, and if the groove route interval is reduced, welding cracks are likely to occur.
【０００４】これらの欠点のために、溶接能率の向上が
阻害され、継ぎ手の健全性が損なわれるという難点があ
る。[0004] These drawbacks hinder the improvement of welding efficiency and impair the integrity of the joint.
【０００５】本発明はかかる問題点に鑑みてなされたも
のであって、溶接能率又は継ぎ手の健全性等に関する従
来技術の欠点を解消し、高能率で且つ耐割れ性、ビード
外観形状及び溶接金属の機械的性能が優れた継ぎ手が得
られる横向片面ガスシールドアーク溶接方法を提供する
ことを目的とする。The present invention has been made in view of the above problems, and solves the drawbacks of the prior art relating to welding efficiency or soundness of a joint, and has a high efficiency and crack resistance, a bead appearance shape, and a weld metal. It is an object of the present invention to provide a horizontal one-sided gas shielded arc welding method capable of obtaining a joint having excellent mechanical performance.
【０００６】[0006]
【課題を解決するための手段】本発明に係るガスシール
ドアーク溶接方法は、直径が１．２乃至２．０ｍｍのソ
リッドワイヤ又はフラックス入りワイヤを、シールドガ
ス及び裏当て材と組み合わせて行う横向片面ガスシール
ドアーク溶接方法において、ルート間隔が０で、表側が
開いた開先を設け、開先裏側に裏当て材を設け、表側に
て開先の下半部に１０乃至２５ｍｍの長さで介在する表
当材を設け、１パス目のワイヤ狙い位置を下板開先上で
鋼板裏面から開先面に沿って２乃至１２ｍｍの範囲に設
定し、２８０Ａ以上の溶接電流でストリンガ溶接又はウ
ィービング溶接をすることを特徴とする。SUMMARY OF THE INVENTION A gas shielded arc welding method according to the present invention is a horizontal one-sided method in which a solid wire or a flux-cored wire having a diameter of 1.2 to 2.0 mm is combined with a shielding gas and a backing material. in gas shielded arc welding method, the root gap is zero, the front side is opened GMA provided, the backing material provided in groove back, intervening length of 10 to 25mm in the lower half of the groove at the front side The target position of the first pass wire is set in the range of 2 to 12 mm along the groove from the back of the steel plate on the lower plate groove, and stringer welding or weaving welding with a welding current of 280 A or more. It is characterized by doing.
【０００７】[0007]
【作用】本願発明者等は、前述の従来技術の欠点を解消
すべく種々実験研究を繰り返した結果、特許請求の範囲
にて規定した条件でガスシールドアーク溶接することに
より、本発明の目的を達成できることを見い出した。The inventors of the present invention have conducted various experimental studies to solve the above-mentioned disadvantages of the prior art, and as a result, have achieved the object of the present invention by performing gas shielded arc welding under the conditions specified in the claims. I found what I could achieve.
【０００８】なお、本発明においては、図１にその一例
を示すように、上方の上板１と下方の下板２とを被溶接
材として上下に配置し、その突き合わせ端部に、Ｖ字形
又はＹ字形の開先４を設ける。上板１及び下板２の裏面
における開先４の間隔（ルート間隔）は実質的に０であ
り、上板１及び下板２の表面側で開先４が開いている。
そして、上板１及び下板２の裏面にて開先部に裏当材３
をあてがい、開先４の表面側にて表当材５をその開先の
下半部に介在するように設ける。この表当材５の開先内
突出高さ、即ち、開先下半部に介在する長さは１０乃至
２５ｍｍである。In the present invention, as shown in FIG. 1, an upper upper plate 1 and a lower lower plate 2 are vertically arranged as a material to be welded, and a V-shaped end is formed at the abutting end thereof. Alternatively, a Y-shaped groove 4 is provided. The gap (route interval) between the grooves 4 on the back surfaces of the upper plate 1 and the lower plate 2 is substantially 0, and the groove 4 is open on the surface side of the upper plate 1 and the lower plate 2.
Then, a backing material 3 is provided on the groove at the back surface of the upper plate 1 and the lower plate 2.
The front contact material 5 is provided on the surface side of the groove 4 so as to be interposed in the lower half of the groove. The protruding height of the front contact material 5 in the groove, that is, the length interposed in the lower half of the groove is 10 to 25 mm.
【０００９】以下、本発明における各数値の限定理由に
ついて説明する。（１）ワイヤ径：直径１．２乃至２．０ｍｍ ワイヤ径が１．２ｍｍ未満の細径ワイヤでは、単位長さ
当たりの重量が小さいため、市販の溶接電源で使用する
場合は、ワイヤ送給速度を上限に設定しても高溶着量が
得られない。また、アークの広がりが小さいため、ワイ
ヤの狙い位置がずれた場合に融合不良などの溶接欠点が
発生し易い。更に、ワイヤの剛性が低いため、座屈等の
送給不良が発生しやすく、これもまた溶接欠陥の発生に
繋がる。The reasons for limiting each numerical value in the present invention will be described below. (1) Wire diameter: 1.2 to 2.0 mm in diameter. A small diameter wire having a wire diameter of less than 1.2 mm has a small weight per unit length. Even if the speed is set to the upper limit, a high welding amount cannot be obtained. Further, since the spread of the arc is small, welding defects such as poor fusion are likely to occur when the target position of the wire is shifted. Furthermore, since the rigidity of the wire is low, poor feeding such as buckling is likely to occur, which also leads to the occurrence of welding defects.
【００１０】ワイヤ径が２．０ｍｍを超えると、太径ワ
イヤを市販の溶接電源で使用する場合、容量（溶接電流
の上限）が小さく、ワイヤ送給速度を増大できないた
め、高溶着量が得られない。また、ワイヤの剛性が高い
ため、送給の安定性が低下し、融合不良等の溶接欠陥が
発生しやすくなる。従って、ワイヤの直径は１．２乃至
２．０ｍｍとする。When the wire diameter exceeds 2.0 mm, when a large-diameter wire is used with a commercially available welding power source, the capacity (the upper limit of the welding current) is small and the wire feeding speed cannot be increased, so that a high welding amount can be obtained. I can't. In addition, since the rigidity of the wire is high, the feeding stability is reduced, and welding defects such as poor fusion are likely to occur. Therefore, the diameter of the wire is set to 1.2 to 2.0 mm.
【００１１】（２）開先ルート間隔：実質的に０ｍｍ 開先断面積を低減して溶接時間を短縮すると共に、ルー
ト間隔の管理を省略して、溶接施工全体の能率向上を図
るため、開先ルート間隔は０ｍｍとする。 (2) Groove route interval: In order to shorten the welding time by substantially reducing the groove cross-sectional area by 0 mm and to omit the management of the route interval to improve the efficiency of the entire welding work, The leading route interval is 0 mm.
【００１２】（３）１パス目のワイヤ狙い位置：下板開
先上で鋼板裏面から開先面に沿って２乃至１２ｍｍの位
置 この１パス目のワイヤ狙い位置が２ｍｍ未満ではアーク
によって開先が過度に溶融されるため、裏波ビードの止
端にアンダーカットが発生したり、溶融池が溶け落ちる
という不都合がある。 (3) Target position of the first pass wire: lower plate open
2mm to 12mm along the groove from the back of the steel plate
For location the first pass of the wire aim positions that GMA is melted excessively by the arc is less than 2 mm, or undercutting occurs toe of the penetration bead, there is a disadvantage that the molten pool falls melted.
【００１３】一方、狙い位置が１２ｍｍを超えると、開
先はアークによって溶融され難くなるため、良好な裏波
ビートが形成されず、場合によっては割れが発生する。On the other hand, if the target position exceeds 12 mm, the groove is hardly melted by the arc, so that a good back wave beat is not formed, and in some cases, cracks occur.
【００１４】従って、１パス目のワイヤ狙い位置は下板
開先裏面から２乃至１２ｍｍとする。Therefore, the target position of the wire in the first pass is 2 to 12 mm from the back surface of the groove of the lower plate.
【００１５】（４）１パス目の運棒：ストリンガ溶接又
はウィービング溶接 ストリンガ溶接ではウィービング溶接に比してスパッタ
発生量が若干少なく、且つ溶接装置もウィーバの省略等
により小型・軽量化が可能である。このため、開先のル
ート間隔が実質的に０ｍｍ又はそれに近く、溶接条件と
の組み合わせにおいて形状が良好で且つ耐割れ性が優れ
た裏波ビードが形成される場合は、ストリンガ溶接（ウ
ィービングなし）を行う。 (4) Rod in the first pass: stringer welding or
In the weaving welding stringer welding, the amount of spatter generated is slightly smaller than that in the weaving welding, and the welding device can be reduced in size and weight by omitting the weaver. For this reason, in the case where the root spacing of the groove is substantially 0 mm or close thereto and a Uranami bead having a good shape and excellent cracking resistance is formed in combination with welding conditions, stringer welding (without weaving) I do.
【００１６】一方、開先の加工精度不良等によって、ル
ート間隔が広くなり、溶接条件との組み合わせにおいて
も裏波ビードのアンダーカット又は溶融池の溶け落ちが
防止できない場合は、ウィービング溶接を行う。On the other hand, when the root interval is widened due to poor machining accuracy of the groove and the like, the undercut of the Uranami bead or the meltdown of the molten pool cannot be prevented even in combination with the welding conditions, weaving welding is performed.
【００１７】（５）溶融金属の漏れ止め材として、表当
材を図１に示すように配置する。 図１に示すように、この表当材５は開先４内に盛られる
溶融金属の漏れ止めとして機能する。仕上げ層の溶接
は、通常、溶融金属の垂れ防止等の観点より、高電流且
つ低速度による高溶着量化が困難であった。しかし、溶
融金属の漏れ止め材として、本発明は表当材５を使用す
るので、高溶着量の溶接が可能になる。この場合、表当
材５の上端は開先下端よりも１０ｍｍ以上、２５ｍｍ以
下の範囲で開先下半部に突出させる。 (5) As a material for preventing molten metal from leaking,
The materials are arranged as shown in FIG. As shown in FIG. 1, the dressing 5 functions as a leak preventer for the molten metal piled in the groove 4. In the welding of the finishing layer, it is usually difficult to increase the amount of deposition at a high current and a low speed from the viewpoint of preventing the molten metal from dripping. However, since the present invention uses the front contact material 5 as a material for preventing the molten metal from leaking, welding with a high welding amount becomes possible. In this case, the upper end of the front contact material 5 is projected to the lower half of the groove within a range of 10 mm or more and 25 mm or less from the lower end of the groove.
【００１８】表当材の突出量が１０ｍｍ未満では、漏れ
止め効果が最下段パスのみに限定される。次のパス以降
も高溶着量の溶接が可能となるようにするため、突出量
は１０ｍｍ以上とする。If the protruding amount of the front contact material is less than 10 mm, the leakage preventing effect is limited to only the lowermost pass. In order to enable welding with a high welding amount after the next pass, the protrusion amount is set to 10 mm or more.
【００１９】表当材の突出量が２５ｍｍを超えると、最
下段パスのワイヤ狙い位置が表当材との干渉によって適
正範囲から外れるため、融合不良又はビード外観・形状
不良等の欠陥が発生する。従って、表当材の突出量は開
先下端よりも１０乃至２５mmとする。If the protruding amount of the cover material exceeds 25 mm, the target position of the wire in the lowermost pass deviates from an appropriate range due to interference with the cover material, and defects such as defective fusion or defective bead appearance and shape occur. . Therefore, the projecting amount of the front contact material is set to 10 to 25 mm from the lower end of the groove.
【００２０】（６）ワイヤ化学成分（フラックス入りワ
イヤ及びソリッドワイヤ） Ｃ：０．０１乃至０．２０重量％ Ｃ（炭素）は良好な裏波ビードの形成、裏波溶接ビード
の割れ防止、溶接金属の機械的性能の調整等の目的で添
加する。 (6) Wire chemical components (flux-containing
(Ear and solid wire) C: 0.01 to 0.20% by weight C (carbon) is added for the purpose of forming a good backside bead, preventing cracking of the backside weld bead, and adjusting the mechanical performance of the weld metal. I do.
【００２１】Ｃが０．０１重量％未満ではアーク中の電
位傾度が小さいため、適正アーク長での溶接電圧は低く
なる。これによって溶込み深さが小さくなり、裏波ビー
ドの形成が困難となる。また、Ｃは溶接金属の焼入れ性
を高める元素であるが、０．０１重量％未満では、フェ
ライト粒が粗大化するため、裏波溶接ビードに割れが発
生しやすくなる。更に、溶接金属の強度及び靱性が母材
に対して不十分となる。When C is less than 0.01% by weight, the potential gradient in the arc is small, so that the welding voltage at an appropriate arc length is low. This reduces the penetration depth and makes it difficult to form a penetration bead. C is an element that enhances the hardenability of the weld metal, but if it is less than 0.01% by weight, the ferrite grains are coarsened, so that cracks are likely to occur in the Uranami weld bead. Furthermore, the strength and toughness of the weld metal are insufficient for the base metal.
【００２２】Ｃが０．２０重量％を超えると、Ｐ，Ｓ等
の不純物の固溶限が小さいオーステナイト相の析出が増
加し、粒界の不純物濃度が増大する。また、溶融金属の
凝固温度範囲が拡大する。これらの影響により、特に裏
波溶接ビードに割れが発生しやすくなる。一方、強度の
増加により、溶接金属の靱性が母材に対して不十分とな
る。更に、溶滴又は溶融池の中でＣＯが発生し易くな
る。溶滴中のＣＯは爆発して多量のスパッタが生じ、溶
融地内のＣＯはブローホール又はピット等の気孔欠陥を
生じる。従って、ワイヤ中のＣ量は０．０１乃至０．２
０重量％とする。When C exceeds 0.20% by weight, precipitation of an austenite phase having a small solid solubility limit of impurities such as P and S increases, and the impurity concentration at grain boundaries increases. Further, the solidification temperature range of the molten metal is expanded. Due to these effects, cracks particularly easily occur in the Uranami weld bead. On the other hand, the increase in strength makes the toughness of the weld metal insufficient for the base metal. Further, CO is easily generated in the droplet or the molten pool. The CO in the droplet explodes to generate a large amount of spatter, and the CO in the molten ground causes pore defects such as blow holes or pits. Therefore, the C content in the wire is 0.01 to 0.2.
0% by weight.
【００２３】Ｓｉ：０．２０〜１．５０重量％ Ｓｉ（シリコン）は良好な裏波ビードの形成、気孔欠陥
の発生防止、溶接金属の機械的性能の調整等の目的で添
加する。Si: 0.20 to 1.50% by weight Si (silicon) is added for the purpose of forming a good backside bead, preventing the generation of pore defects, adjusting the mechanical performance of the weld metal, and the like.
【００２４】Ｓｉが０．０１重量％未満では、母材への
ビードのなじみが劣化し、特に裏波ビードの形状不良が
生じる。また、他の脱酸剤の添加量が不十分な場合には
気孔欠陥が発生し易い。更に、溶接金属の強度が母材に
対して不足する。If the content of Si is less than 0.01% by weight, the adaptation of the bead to the base material is deteriorated, and particularly, the shape defect of the Uranami bead occurs. Further, when the amount of the other deoxidizing agent is insufficient, pore defects are likely to occur. Further, the strength of the weld metal is insufficient with respect to the base metal.
【００２５】Ｓｉが１．５０重量％を超えると、溶接金
属の強度が過剰となり、靱性が母材に対して不十分とな
る。従って、ワイヤ中のＳｉ量は０．２０乃至１．５０
重量％とする。When Si exceeds 1.50% by weight, the strength of the weld metal becomes excessive and the toughness becomes insufficient with respect to the base metal. Therefore, the amount of Si in the wire is 0.20 to 1.50.
% By weight.
【００２６】Ｍｎ：０．２０〜２．５０重量％ Ｍｎ（マンガン）は裏波溶接ビードの割れ防止、気孔欠
陥の発生防止、溶接金属の機械的性能の調整等の目的で
添加する。Mn: 0.20 to 2.50% by weight Mn (manganese) is added for the purpose of preventing cracking of the backside weld bead, preventing generation of pore defects, adjusting the mechanical performance of the weld metal, and the like.
【００２７】ＭｎはＣと同様に溶接金属の焼入れ性を高
め、且つ不純物であるＳとＭｎＳを形成する。しかし、
Ｍｎ含有量が０．２０重量％未満では、これらの効果が
不十分であり、フェライト粒が粗大化したり、最終凝固
域のＳ量が減少しないため、特に裏波溶接ビードに割れ
が発生し易くなる。また、他の脱酸剤の添加量が不十分
な場合には気孔欠陥が発生し易い。更に、溶接金属の強
度及び靱性が母材に対して不足する。Mn, like C, enhances the hardenability of the weld metal and forms impurities S and MnS. But,
If the Mn content is less than 0.20% by weight, these effects are insufficient, and the ferrite grains are not coarsened and the S content in the final solidification region is not reduced. Become. Further, when the amount of the other deoxidizing agent is insufficient, pore defects are likely to occur. Further, the strength and toughness of the weld metal are insufficient for the base metal.
【００２８】Ｍｎ含有量が２．５０重量％を超えると、
溶接金属の強度が過剰となり、靱性が母材に対して不十
分となる。従って、ワイヤ中のＭｎ量は０．２０乃至
２．５０重量％とする。When the Mn content exceeds 2.50% by weight,
The strength of the weld metal becomes excessive and the toughness becomes insufficient for the base metal. Therefore, the amount of Mn in the wire is set to 0.20 to 2.50% by weight.
【００２９】Ｔｉ：０．０１〜０．５０重量％ Ｔｉ（チタン）は良好な裏波ビードの形成、気孔欠陥の
発生防止、溶接金属の機械的性能の調整等の目的で添加
する。Ti: 0.01 to 0.50% by weight Ti (titanium) is added for the purpose of forming a good backside bead, preventing the occurrence of pore defects, adjusting the mechanical performance of the weld metal, and the like.
【００３０】Ｔｉ含有量が０．０１重量％未満では脱酸
が不足して溶滴の酸素量が高くなるため、表面張力が低
下して形状が伸長し、溶融池との不規則な短絡が増加す
る。これによって溶融池の形状又は溶融金属の対流が不
安定となる。また、短絡時にアークが消失するため、溶
融池の温度又は入熱量が低下する。これらの影響によ
り、良好な裏波ビードの形成が困難になる。If the Ti content is less than 0.01% by weight, deoxidation becomes insufficient and the oxygen content of the droplet becomes high, so that the surface tension is reduced, the shape is elongated, and an irregular short circuit with the molten pool occurs. To increase. This makes the shape of the molten pool or the convection of the molten metal unstable. In addition, since the arc disappears during a short circuit, the temperature or heat input of the molten pool decreases. These effects make it difficult to form good backwash beads.
【００３１】Ｔｉ量が０．５０重量％を超えると、固い
スラグがビード全面を覆うため、スラグ除去又は連続溶
接等の溶接性が低下する。また、溶接金属の強度が過剰
となり、靱性が母材に対して不十分となる。従って、ワ
イヤ中のＴｉ量は０．０１乃至０．５０重量％とする。If the amount of Ti exceeds 0.50% by weight, hard slag covers the entire surface of the bead, and the weldability such as slag removal or continuous welding is reduced. Further, the strength of the weld metal becomes excessive and the toughness becomes insufficient with respect to the base metal. Therefore, the amount of Ti in the wire is set to 0.01 to 0.50% by weight.
【００３２】Ｎａ，Ｋ，Ｃｅ化合物：Ｎａ，Ｋ，Ｃｅ
に換算した合計が フラックス入りワイヤの場合：０．００５〜０．３５重
量％ ソリッドワイヤの場合：０．００００２重量〜０．００
３重量％ Ｎａ，Ｋ，Ｃｅ化合物は、アーク及び溶滴移行を安定化
する目的で添加する。Na, K, Ce compounds: Na, K, Ce
In the case of flux-cored wire: 0.005 to 0.35% by weight In the case of solid wire: 0.00002% to 0.00
The 3 wt% Na, K, Ce compound is added for the purpose of stabilizing arc and droplet transfer.
【００３３】ソリッドワイヤに関しては、これらの化合
物は必要に応じてワイヤ表面へ塗布することにより添加
する。With respect to solid wires, these compounds are added by applying to the wire surface as required.
【００３４】（ａ）フラックス入りワイヤ：０．００５
〜０．３５重量％ ０．００５重量％未満ではアーク及び溶滴移行が不安定
であり、それによって溶融池の安定性も低下する。この
ため、特に裏波ビードの形状不良が顕著となる。また、
スパッタ発生量の増加又はビード外観・形状の劣化が生
じる。(A) Flux-cored wire: 0.005
If it is less than 0.005% by weight, arc and droplet transfer are unstable, and the stability of the molten pool also decreases. For this reason, the shape defect of the Uranami bead becomes remarkable. Also,
An increase in the amount of spatter or deterioration of the bead appearance / shape occurs.
【００３５】０．３５重量％を超えると、Ｎａ，Ｋ，Ｃ
ｅ化合物の蒸気圧が高いために、アーク中の蒸気圧が過
度に上昇する。これによって、アーク力が低下し、溶込
み形状が不安定で且つ浅くなるため、裏波ビードの形状
が劣化する。また、移行する溶滴径が大きくなるため、
大粒のスパッタが多量に発生する。If it exceeds 0.35% by weight, Na, K, C
Due to the high vapor pressure of the e-compound, the vapor pressure in the arc increases excessively. As a result, the arc force decreases, and the penetration shape becomes unstable and shallow, so that the shape of the Uranami bead deteriorates. In addition, since the diameter of the droplet that migrates increases,
Large amounts of large spatters are generated.
【００３６】従って、フラックス入りワイヤ中のＮａ，
Ｋ，Ｃｅ化合物の添加量は、Ｎａ，Ｋ，Ｃｅに換算して
その合計で０．００５乃至０．３５重量％とする。Accordingly, Na, in the flux-cored wire,
The added amount of the K and Ce compounds is 0.005 to 0.35% by weight in total in terms of Na, K and Ce.
【００３７】（ｂ）ソリッドワイヤ：０．００００２〜
０．００３重量％ ソリッドワイヤにＮａ，Ｋ，Ｃｅ化合物を添加する場合
は、主としてワイヤ表面にその化合物を塗布する。通
常、アークはワイヤ表面から発生するので、表面に塗布
されたＮａ，Ｋ，Ｃｅ化合物はアーク安定化に有効に作
用する。(B) Solid wire: 0.00002-
When adding a Na, K, Ce compound to a 0.003% by weight solid wire, the compound is mainly applied to the wire surface. Usually, since an arc is generated from the wire surface, the Na, K, Ce compound applied to the surface effectively acts on the arc stabilization.
【００３８】０．００００２重量％未満では、アーク及
び溶滴移行を安定化する顕著な効果が得られない。If the amount is less than 0.00002% by weight, a remarkable effect of stabilizing arc and droplet transfer cannot be obtained.
【００３９】０．００３重量％を超えると、ワイヤ表面
の付着量が増加するため、それらがワイヤ送給経路の中
に堆積し、ワイヤの送給性を低下させる。従って、ソリ
ッドワイヤへのＮａ，Ｋ，Ｃｅ化合物の添加量は、Ｎ
ａ，Ｋ，Ｃｅの合計で０．００００２乃至０．００３重
量％とし、必要に応じてワイヤ表面へ塗布する。When the content exceeds 0.003% by weight, the amount of adhesion on the surface of the wire increases, so that they accumulate in the wire feeding path and lower the wire feedability. Therefore, the amount of the Na, K, Ce compound added to the solid wire is N
The total of a, K, and Ce is 0.00002 to 0.003% by weight, and is applied to the wire surface as needed.
【００４０】Ａｌ、Ｍｇ：合計で０．０５〜１．００
重量％ Ａｌ及びＭｇは、溶接金属の酸素量を低減して靱性を向
上させることを目的として、必要に応じて添加する。な
お、ソリッドワイヤへのＭｇの添加は、鉄地表面にＭｇ
又はＭｇ化合物の粉末を塗布し、その上からＣｕメッキ
を施して覆うなどの手段によって行う。Al, Mg: 0.05 to 1.00 in total
Weight% Al and Mg are added as necessary for the purpose of reducing the oxygen content of the weld metal and improving the toughness. In addition, the addition of Mg to the solid wire
Alternatively, it is performed by a method such as applying a powder of a Mg compound and applying a Cu plating thereon to cover.
【００４１】Ａｌ及び／又はＭｇが０．０５重量％未満
では、溶接金属の靱性向上に顕著な効果は認められな
い。If Al and / or Mg is less than 0.05% by weight, no remarkable effect on improving the toughness of the weld metal is not recognized.
【００４２】Ａｌ及び／又はＭｇが１．００重量％を超
えると、Ａｌ及びＭｇの蒸気圧が高いため、アーク中の
蒸気圧が過度に上昇する。これによってヒューム発生量
が増加したり、移行する溶滴径が大きくなるため大粒の
スッパタが多量に発生し、作業性が低下する。従って、
ワイヤ中のＡｌ及びＭｇ量は、合計で０．０５乃至１．
００重量％とする。If the content of Al and / or Mg exceeds 1.00% by weight, the vapor pressure of Al and Mg is too high, so that the vapor pressure in the arc increases excessively. As a result, the amount of generated fumes increases, and the diameter of the transferred droplets increases, so that a large amount of large spatter is generated and the workability is reduced. Therefore,
The total amount of Al and Mg in the wire is 0.05 to 1.
00% by weight.
【００４３】Ｎｉ：０．１０〜４．００重量％ Ｎｉは、溶接金属中のオーステナイト量を増加して靱性
を向上させることを目的とし、必要に応じて添加する。Ni: 0.10 to 4.00% by weight Ni is added as required for the purpose of increasing the amount of austenite in the weld metal to improve toughness.
【００４４】Ｎｉが０．１０重量％未満では、溶接金属
の靱性向上に顕著な効果は認められない。Ｎｉが４．０
０重量％を超えると、Ｃと同様にＰ，Ｓ等不純物の固溶
限が小さくなるため、オーステナイト相の析出が増加
し、粒界の不純物濃度が増大する。また、低融点のＮｉ
Ｓが形成される。これらの影響により、特に裏波溶接ビ
ードに割れが発生しやすくなる。従って、ワイヤ中のＮ
ｉ量は０．１０乃至４．００重量％とする。If Ni is less than 0.10% by weight, no remarkable effect on improving the toughness of the weld metal is not recognized. Ni is 4.0
When the content exceeds 0% by weight, the solid solubility limit of impurities such as P and S becomes small like C, so that the precipitation of austenite phase increases and the impurity concentration at grain boundaries increases. In addition, low melting point Ni
S is formed. Due to these effects, cracks particularly easily occur in the Uranami weld bead. Therefore, N in the wire
The i amount is 0.10 to 4.00% by weight.
【００４５】（７）表当材（溶融金属の漏れ止め材）の
化学成分 固形物の耐火性及びスラグの粘度、表面張力並びに流動
性等を調整して、ビード外観・形状を整えること、及び
スラグ剥離性を良好にすることを目的として、Ｓｉ
Ｏ2、Ａｌ2Ｏ3、ＣａＯ、ＭｇＯ、ＺｒＯ2等を適量含有
する耐火物で成形する。これらの化学成分の含有量は以
下のとおりである。(7) The chemical composition of the dressing material (leak stopper for molten metal): adjusting the fire resistance of the solid material and the viscosity, surface tension, fluidity, etc. of the slag to adjust the appearance and shape of the bead; and In order to improve the slag removability, Si
A refractory containing an appropriate amount of O 2 , Al 2 O 3 , CaO, MgO, ZrO 2 or the like is formed. The contents of these chemical components are as follows.
【００４６】ＳｉＯ2：３０．０〜６０．０重量％ ＳｉＯ2が３０．０重量％未満では、固形物の耐火性が
不足して溶融量が多くなるため、仕上げビードの余盛り
が過大なる。これにより、ビード形状が劣化すると共
に、開先断面積の残し量が増加して溶接の能率が低下す
る。SiO 2 : 30.0 to 60.0% by weight When the content of SiO 2 is less than 30.0% by weight, the fire resistance of the solid is insufficient and the amount of melting is increased, so that the excess of the finished bead becomes excessive. . As a result, the bead shape is deteriorated, and the remaining amount of the groove cross section is increased, so that the efficiency of welding is reduced.
【００４７】ＳｉＯ2が６０．０重量％を超えるとスラ
グの流動性が過大となり、アンダーカット又はスラグ巻
き込み等の欠陥が発生したり、ビードの外観・形状が不
均一になる。従って、耐火物中のＳｉＯ2量は３０．０
乃至６０．０重量％とする。If the content of SiO 2 exceeds 60.0% by weight, the fluidity of the slag becomes excessive, and defects such as undercut or slag entrainment occur, and the appearance and shape of the bead become uneven. Therefore, the amount of SiO 2 in the refractory is 30.0%.
To 60.0% by weight.
【００４８】Ａｌ2Ｏ3：５．０〜４０．０重量％ Ａｌ2Ｏ3が５．０重量％未満では、ＳｉＯ2と同様に固
形物の耐火性が不足するため、仕上げたビード余盛りが
過大となる。これにより、ビード形状が劣化すると共
に、開先断面積の残し量が増加して溶接の能率が低下す
る。Al 2 O 3 : 5.0 to 40.0% by weight When the content of Al 2 O 3 is less than 5.0% by weight, the fire resistance of the solid material is insufficient as in the case of SiO 2. Becomes excessive. As a result, the bead shape is deteriorated, and the remaining amount of the groove cross section is increased, so that the efficiency of welding is reduced.
【００４９】Ａｌ2Ｏ3が４０．０重量％を超えると耐火
性が過剰となり、仕上げビードの余盛りは小さくなる。
この場合、表当材が作用しない部分との境にオーバラッ
プが発生する。従って、耐火物中のＡｌ2０3量は５．０
乃至４０．０重量％とする。If the content of Al 2 O 3 exceeds 40.0% by weight, the fire resistance becomes excessive, and the margin of the finished bead becomes small.
In this case, an overlap occurs at the boundary with the portion where the front dressing does not act. Therefore, Al 2 0 3 content in the refractory is 5.0
To 40.0% by weight.
【００５０】ＣａＯ：０．０１〜４０．０重量％ ＣａＯが０．０１重量％未満では、ＳｉＯ2、Ａｌ2０3
と同様に固形物の耐火性が不足するため、仕上げビード
の余盛りが過大となる。これにより、ビード形状が劣化
すると共に、開先断面積の残し量が増加し溶接の能率が
低下する。また、スラグの表面張力が高くなって被りが
劣化するため、ビード外観不良が生じる。CaO: 0.01 to 40.0% by weight When CaO is less than 0.01% by weight, SiO 2 , Al 2 O 3
In the same manner as in the above, the fire resistance of the solid material is insufficient, so that the margin of the finished bead becomes excessive. As a result, the bead shape is deteriorated, and the remaining amount of the groove cross-sectional area is increased, and the welding efficiency is reduced. In addition, since the surface tension of the slag increases and the fogging deteriorates, poor bead appearance occurs.
【００５１】ＣａＯが４０．０重量％を超えると、Ａｌ
2Ｏ3と同様に耐火性が過剰となり、仕上げビードの余盛
りが小さくなるため、表当材が作用しない部分との境に
オーバラップが発生する。従って、耐火物中のＣａＯ量
は０．０１乃至４０．０重量％とする。When CaO exceeds 40.0% by weight, Al
As in the case of 2 O 3 , the fire resistance becomes excessive, and the margin of the finished bead becomes small, so that an overlap occurs at the boundary with the portion where the dressing material does not act. Therefore, the amount of CaO in the refractory is set to 0.01 to 40.0% by weight.
【００５２】ＭｇＯ：０．０１〜２０．０重量％ ＭｇＯが０．０１重量％未満では、ＳｉＯ2、Ａｌ
2Ｏ3、ＭｇＯと同様に固形物の耐火性が不足するため、
仕上げビードの余盛りが過大となる。これにより、ビー
ド形状が劣化すると共に、開先断面積の残し量が増加し
て溶接の能率が低下する。また、スラグ剥離性が劣化す
る。MgO: 0.01 to 20.0% by weight When MgO is less than 0.01% by weight, SiO 2 , Al
As with 2 O 3 and MgO, the fire resistance of solids is insufficient.
Excessive finishing beads are excessive. As a result, the bead shape is deteriorated, and the remaining amount of the groove cross section is increased, so that the efficiency of welding is reduced. In addition, the slag removability deteriorates.
【００５３】一方、ＭｇＯが２０．０重量％を超える
と、Ａｌ2Ｏ3、ＣａＯと同様に耐火性が過剰となり、仕
上げビードの余盛りが小さくなるため、表当材が作用し
ない部分との境にオーバラップが発生する。従って、耐
火物中のＭｇＯ量は０．０１重量％以上２０．０重量％
以下とする。On the other hand, if the content of MgO exceeds 20.0% by weight, the fire resistance becomes excessive similarly to Al 2 O 3 and CaO, and the margin of the finished bead becomes small. Overlap occurs at the boundary. Therefore, the amount of MgO in the refractory is 0.01% by weight to 20.0% by weight.
The following is assumed.
【００５４】ＺｒＯ2：０．０１〜２０．０重量％ ＺｒＯ2はＳｉＯ2，Ａｌ2Ｏ3，ＭｇＯ，ＭｇＯと同様に
固形物の耐火性を調整し、仕上げビードの余盛りを適正
化する。余盛りはＺｒＯ2が０．０１重量％未満の場合
に過大、２０．０重量％を超えると過小となる。従っ
て、耐火物中のＺｒＯ2量は０．０１乃至２０．０重量
％とする。ZrO 2 : 0.01 to 20.0% by weight ZrO 2 adjusts the fire resistance of the solid material in the same manner as SiO 2 , Al 2 O 3 , MgO and MgO, and optimizes the margin of the finished bead. . The excess is too large when ZrO 2 is less than 0.01% by weight, and too small when ZrO 2 exceeds 20.0% by weight. Therefore, the amount of ZrO 2 in the refractory is set to 0.01 to 20.0% by weight.
【００５５】[0055]
【実施例】以下、本発明の実施例についてその比較例と
比較して説明する。下記表１は溶接条件を示す。また、
表２乃至表４は使用したワイヤ組成及びワイヤ径を示
す。このワイヤの種類としては、ワイヤＮｏ．ＷＦ１〜
ＷＦ４１と、ワイヤＮｏ．ＷＳ１〜ＷＳ９があり、それ
らの一部が実施例、残部が比較例である。更に、下記表
５は表当材を構成する耐火物の化学成分を示す。この表
当材はＮｏ．Ｆ１〜Ｆ１７まであり、それらの一部が実
施例、残部が比較例である。表６は初層の溶接条件を示
すものであり、この初層溶接条件はＮｏ．１〜７６まで
ある。表７は板厚１６ｍｍでの溶接条件を示すものであ
り、この板厚１６ｍｍでの溶接条件はＮｏ．１〜５３ま
である。表８は表６の初層の溶接条件におけるアーク安
定性等の特性の評価結果を示すものである。表９は板厚
１６ｍｍでの溶接条件におけるアーク安定性等の特性の
評価結果を示すものである。 EXAMPLES Examples of the present invention will be described below in comparison with comparative examples. Table 1 below shows the welding conditions. Also,
Tables 2 to 4 show the wire compositions and wire diameters used.
You. As the type of this wire, wire No. WF1
WF41 and wire No. There are WS1-WS9, which
Some of these are examples and the rest are comparative examples. In addition, the following table
Reference numeral 5 denotes a chemical component of the refractory constituting the front dressing material. This table
This material is No. F1 to F17, some of which are real
Examples and the rest are comparative examples. Table 6 shows the welding conditions for the first layer.
The first layer welding conditions are No. From 1 to 76
is there. Table 7 shows welding conditions at a plate thickness of 16 mm.
No., the welding conditions at this plate thickness of 16 mm 1 to 53
It is. Table 8 shows the arc resistance under the welding conditions for the first layer in Table 6.
It shows the evaluation results of characteristics such as qualitative properties. Table 9 shows sheet thickness
Characteristics such as arc stability under welding conditions at 16 mm
It shows an evaluation result.
【００５６】[0056]
【表１】 [Table 1]
【００５７】[0057]
【表２】 [Table 2]
【００５８】[0058]
【表３】 [Table 3]
【００５９】[0059]
【表４】 [Table 4]
【００６０】[0060]
【００６１】[0061]
【表５】 [Table 5]
【００６２】[0062]
【表６】 [Table 6]
【００６３】[0063]
【表７】 [Table 7]
【００６４】[0064]
【表８】 初層の溶接条件は表６を参照。 [Table 8] See Table 6 for the first layer welding conditions.
【００６５】[0065]
【表９】 溶接条件は表７を参照。 [Table 9] See Table 7 for welding conditions.
【００６６】これらの表８に示すように、本発明の条件
を満足する実施例の場合には、初層の溶接において、ア
ーク安定性、裏波ビードの外観形状、スパッタ発生量、
耐割れ性の全てが優れていた。これに対し、本発明の条
件から外れる比較例の場合には、これらの性能のいずれ
かが劣るものであった。As shown in Table 8, in the case of the embodiment satisfying the conditions of the present invention, in the welding of the first layer, the arc stability, the appearance of the Uranami bead, the spatter generation amount,
All of the crack resistances were excellent. On the other hand, in the case of the comparative example which did not satisfy the conditions of the present invention, one of these performances was inferior.
【００６７】また、表９から明らかなように、板厚が１
６ｍｍの被溶接材を溶接した場合も、本発明の条件を満
足する実施例の場合には、アーク安定性、ビード外観形
状、スパッタ発生量、初層の耐割れ性、溶接金属の機械
的性質の全ての性能が優れたものであった。これに対
し、本発明の条件から外れる比較例の場合には、これら
のいずれかの性能が劣るものであった。Further, as is apparent from Table 9, the sheet thickness is 1
Even in the case of welding a 6 mm weld material, in the case of the embodiment satisfying the conditions of the present invention, arc stability, bead appearance shape, spatter generation amount, crack resistance of the first layer, mechanical properties of the weld metal All of the performances were excellent. On the other hand, in the case of the comparative example which was out of the conditions of the present invention, any of these performances was inferior.
【００６８】[0068]
【発明の効果】以上説明したように、本発明によれば、
開先ルート間隔を実質的に０とし、１パス目のワイヤ狙
い位置を所定の領域に設定し、表当材を開先内に所定寸
法で突出させて配置したので、横向片面ガスシールドア
ーク溶接において、高能率で、耐割れ性、ビード外観・
形状及び溶接金属の機械的性能が優れた継手を得ること
ができる。As described above, according to the present invention,
Since the groove route interval was set to substantially 0, the wire target position in the first pass was set in a predetermined area, and the front contact material was arranged so as to protrude into the groove with a predetermined size. High efficiency, crack resistance, bead appearance
A joint excellent in shape and mechanical performance of the weld metal can be obtained.
【図１】本発明の一例を示す図である。FIG. 1 is a diagram showing an example of the present invention.
【図２】溶接条件を示す図である。FIG. 2 is a diagram showing welding conditions.
【図３】溶接条件を示す図である。FIG. 3 is a diagram showing welding conditions.
１：上板 ２：下板 ３：裏当材 ４：開先 ５：表当材 1: upper plate 2: lower plate 3: backing material 4: groove 5: front material
フロントページの続き (51)Int.Cl.6 識別記号 ＦＩ Ｂ２３Ｋ 35/368 Ｂ２３Ｋ 35/368 Ｂ Ｃ２２Ｃ 38/00 ３０１ Ｃ２２Ｃ 38/00 ３０１Ｙ 38/14 38/14 (72)発明者 今岡 進 神奈川県藤沢市宮前字裏河内100番１ 株式会社神戸製鋼所藤沢事業所内 (56)参考文献 特開 平５−57434（ＪＰ，Ａ) 特開 昭50−39239（ＪＰ，Ａ) 特開 昭49−20039（ＪＰ，Ａ) (58)調査した分野(Int.Cl.6，ＤＢ名) B23K 9/173 B23K 9/02 B23K 9/035 B23K 33/00 B23K 35/30 320 B23K 35/368 C22C 38/00 301 C22C 38/14 ＩＣＩＲＥＰＡＴContinued on the front page (51) Int.Cl. 6 Identification symbol FI B23K 35/368 B23K 35/368 B C22C 38/00 301 C22C 38/00 301Y 38/14 38/14 (72) Inventor Susumu Imaoka Fujisawa, Kanagawa Prefecture 100-1 Urakawachi, Ichimiyamae, Kobe Steel, Ltd. Fujisawa Works (56) References JP-A-5-57434 (JP, A) JP-A-50-39239 (JP, A) JP-A-49-20039 ( JP, A) (58) Fields investigated (Int. Cl. 6 , DB name) B23K 9/173 B23K 9/02 B23K 9/035 B23K 33/00 B23K 35/30 320 B23K 35/368 C22C 38/00 301 C22C 38/14 ICIREPAT
Claims (6)
ワイヤ又はフラックス入りワイヤを、シールドガス及び
裏当て材と組み合わせて行う横向片面ガスシールドアー
ク溶接方法において、ルート間隔が０で、表側が開いた
開先を設け、開先裏側に裏当て材を設け、表側にて開先
の下半部に１０乃至２５ｍｍの長さで介在する表当材を
設け、１パス目のワイヤ狙い位置を下板開先上で鋼板裏
面から開先面に沿って２乃至１２ｍｍの範囲に設定し、
２８０Ａ以上の溶接電流でストリンガ溶接又はウィービ
ング溶接をすることを特徴とするガスシールドアーク溶
接方法。1. A horizontal single-sided gas shielded arc welding method in which a solid wire or a flux-cored wire having a diameter of 1.2 to 2.0 mm is combined with a shielding gas and a backing material, wherein a root interval is 0 and a front side is open
The GMA is provided, the backing material provided in groove back, the table those wood intervening length of 10 to 25mm in the lower half of the groove at the front side is provided, the lower plate wire aiming position of the first pass On the groove, set the range from 2 to 12 mm along the groove from the back of the steel plate,
A gas shielded arc welding method comprising performing stringer welding or weaving welding with a welding current of 280 A or more.
重量に対し、Ｃ：０．０１〜０．２０重量％、Ｓｉ：
０．２０〜１．５０重量％、Ｍｎ：０．２０〜２．５０
重量％、Ｔｉ：０．０１〜０．５０重量％、Ｎａ，Ｋ，
Ｃｅ化合物：Ｎａ，Ｋ，Ｃｅに換算して合計で０．００
５〜０．３５重量％を含有することを特徴とする請求項
１に記載のガスシールドアーク溶接方法。2. The flux-cored wire has a C content of 0.01 to 0.20% by weight and a Si:
0.20 to 1.50% by weight, Mn: 0.20 to 2.50
Wt%, Ti: 0.01 to 0.50 wt%, Na, K,
Ce compound: 0.00, converted to Na, K, Ce
The gas shielded arc welding method according to claim 1, comprising 5 to 0.35% by weight.
対し、Ｃ：０．０１〜０．２０重量％、Ｓｉ：０．２０
〜１．５０重量％、Ｍｎ：０．２０〜２．５０重量％、
Ｔｉ：０．０１〜０．５０重量％を含有し、残部がＦｅ
及び不可避的不純物からなる組成を有することを特徴と
する請求項１に記載のガスシールドアーク溶接方法。3. The solid wire has a C content of 0.01 to 0.20% by weight and a Si content of 0.20% based on the total weight of the wire.
１．５1.50% by weight, Mn: 0.20 to 2.50% by weight,
Ti: 0.01 to 0.50% by weight, with the balance being Fe
The gas-shielded arc welding method according to claim 1, wherein the gas-shielded arc welding method has a composition including unavoidable impurities.
重量に対し、Ｃ：０．０１〜０．２０重量％、Ｓｉ：
０．２０〜１．５０重量％、Ｍｎ：０．２０〜２．５０
重量％、Ｔｉ：０．０１〜０．５０重量％、Ｎａ，Ｋ，
Ｃｅ化合物：Ｎａ，Ｋ，Ｃｅに換算して合計で０．００
５〜０．３５重量％を含有すると共に、Ａｌ，Ｍｇ：合
計で０．０５〜１．００重量％、Ｎｉ：０．１０〜４．
００重量％の１種又は２種を含有することを特徴とする
請求項１に記載のガスシールドアーク溶接方法。4. The flux-cored wire has a C content of 0.01 to 0.20% by weight and a Si:
0.20 to 1.50% by weight, Mn: 0.20 to 2.50
Wt%, Ti: 0.01 to 0.50 wt%, Na, K,
Ce compound: 0.00, converted to Na, K, Ce
5 to 0.35% by weight, Al and Mg: 0.05 to 1.00% by weight in total, Ni: 0.10 to 4.
The gas shielded arc welding method according to claim 1, wherein one or two kinds of the gas shielded arc are contained at 00% by weight.
対し、Ｃ：０．０１〜０．２０重量％、Ｓｉ：０．２０
〜１．５０重量％、Ｍｎ：０．２０〜２．５０重量％、
Ｔｉ：０．０１〜０．５０重量％、Ｎａ，Ｋ，Ｃｅ化合
物：Ｎａ，Ｋ，Ｃｅに換算して合計で０．００００２〜
０．００３重量％を含有すると共に、Ａｌ，Ｍｇ：合計
で０．０５〜１．００重量％、Ｎｉ：０．１０〜４．０
０重量％の１種又は２種を含有し、残部がＦｅ及び不可
避的不純物からなる組成を有することを特徴とする請求
項１に記載のガスシールドアーク溶接方法。5. The solid wire has a C content of 0.01 to 0.20% by weight and a Si content of 0.20% based on the total weight of the wire.
１．５1.50% by weight, Mn: 0.20 to 2.50% by weight,
Ti: 0.01-0.50% by weight, Na, K, Ce compound: 0.00002- in total in terms of Na, K, Ce
0.003% by weight, Al and Mg: 0.05-1.00% by weight in total, Ni: 0.10-4.0.
The gas shielded arc welding method according to claim 1, wherein the gas shielded arc welding method contains 0% by weight of one or two kinds, and the balance has a composition of Fe and unavoidable impurities.
０．０重量％、Ａｌ2Ｏ3：５．０〜４０．０重量％、Ｃ
ａＯ：０．０１〜４０．０重量、ＭｇＯ：０．０１〜２
０．０重量％、ＺｒＯ2：０．０１〜２０．０重量％か
らなる組成を有する耐火物であることを特徴とする請求
項１乃至５のいずれか１項に記載のガスシールドアーク
溶接方法。6. The dressing material according to claim 6, wherein the SiO 2 is 30.0 to 6%.
0.0% by weight, Al 2 O 3 : 5.0 to 40.0% by weight, C
aO: 0.01 to 40.0 weight, MgO: 0.01 to 2
0.0 wt%, ZrO 2: 0.01 to 20.0 Gas-shielded arc welding method according to any one of claims 1 to 5, characterized in that a refractory having a composition consisting of by weight% .
Priority Applications (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19061794A JP2857329B2 (en) | 1994-08-12 | 1994-08-12 | Gas shielded arc welding method |
| TW084108263A TW287976B (en) | 1994-08-12 | 1995-08-08 | |
| KR1019950024794A KR0180028B1 (en) | 1994-08-12 | 1995-08-11 | Horizontal one-side gas shielded arc welding method and horizontal welding equipment |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP19061794A JP2857329B2 (en) | 1994-08-12 | 1994-08-12 | Gas shielded arc welding method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0852572A JPH0852572A (en) | 1996-02-27 |
| JP2857329B2 true JP2857329B2 (en) | 1999-02-17 |
Family
ID=16261057
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP19061794A Expired - Lifetime JP2857329B2 (en) | 1994-08-12 | 1994-08-12 | Gas shielded arc welding method |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2857329B2 (en) |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3404264B2 (en) * | 1997-09-29 | 2003-05-06 | 株式会社神戸製鋼所 | Solid wire for MAG welding |
| JP5409459B2 (en) * | 2010-03-17 | 2014-02-05 | 日鐵住金溶接工業株式会社 | Flux-cored wire for welding austenitic stainless steel |
| CN102416522B (en) * | 2011-10-14 | 2013-06-12 | 河北首钢燕郊机械有限责任公司 | Welding method of stainless steel thin plate |
| CN110293278A (en) * | 2019-05-06 | 2019-10-01 | 广州文冲船厂有限责任公司 | It is a kind of to pad and pad auxiliary horizontal position welding technique |
| KR102164347B1 (en) * | 2019-05-17 | 2020-10-12 | 정무수 | Ceramic backing material for welding |
| CN111730256B (en) * | 2020-08-31 | 2020-12-04 | 季华实验室 | Weld joint identification method and device based on digital model, storage medium and terminal |
-
1994
- 1994-08-12 JP JP19061794A patent/JP2857329B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0852572A (en) | 1996-02-27 |
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