JPH11207491A - Flux cored wire for co2 gas shielded arc welding using dc straight polarity and welding method thereof - Google Patents
Flux cored wire for co2 gas shielded arc welding using dc straight polarity and welding method thereofInfo
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- JPH11207491A JPH11207491A JP1265498A JP1265498A JPH11207491A JP H11207491 A JPH11207491 A JP H11207491A JP 1265498 A JP1265498 A JP 1265498A JP 1265498 A JP1265498 A JP 1265498A JP H11207491 A JPH11207491 A JP H11207491A
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】本発明は、軟鋼・490 Ｎ／ｍ
ｍ2 級高張力鋼などの炭酸ガスアーク溶接（炭酸ガスを
シールドガスとして用いる溶接）に用いられ、溶接ワイ
ヤを負極とし母材を正極とする直流正極性で使用される
フラックス入り溶接ワイヤに係り、低電流から中電流の
溶接電流範囲（70〜300 Ａ程度）においてスパッタ発生
量が少なく、かつ、靱性の良好な溶接金属が得られ、ま
た、重力の影響によって溶融金属が垂れ下がり易い立向
き・上向き溶接などでの溶接性が良好な直流正極性用炭
酸ガスアーク溶接フラックス入りワイヤ、及び該フラッ
クス入りワイヤを用いた亜鉛めっき鋼板の溶接方法に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a mild steel 490 N / m
used in carbonate gas arc welding, such as m 2 class high strength steel (weld using carbon dioxide gas as shield gas), it relates to a flux-cored welding wire for use in a DC positive polarity to the positive electrode of the base metal and the welding wire and the negative electrode, In the low to medium current welding current range (about 70 to 300 A), a small amount of spatter is generated, and a weld metal with good toughness is obtained. In addition, the molten metal tends to sag under the influence of gravity. The present invention relates to a carbon dioxide gas arc welding flux cored wire for direct current positive polarity having good weldability in welding and the like, and a method for welding a galvanized steel sheet using the flux cored wire.
【０００２】[0002]
【従来の技術】先に、本出願人は、炭酸ガス又は炭酸ガ
スとアルゴンとの混合ガスをシールドガスとするガスシ
ールドアーク溶接で使用されるフラックス入りワイヤに
おいて、アークを安定化させることでスパッタ発生量を
少なくするために、フラックス中にフッ化物としてBaF2
を添加したフッ化バリウム系のフラックス入りワイヤを
提案した（特許第2578483 号公報）。このフッ化バリウ
ム系のフラックス入りワイヤでは、ワイヤを負極（母
材：正極）として直流のアーク溶接を行う直流正極性で
用いられており、直流正極性で使用すると、ワイヤ先端
の溶滴には陽イオンによる衝撃力に加えて、高蒸気圧の
BaF2等の蒸発による大きな反作用力が働くため、ワイヤ
先端の溶滴がこれらの合力により衝撃を受け、小さな溶
滴粒になって母材へとスムーズな移行を行う。これによ
りアークの安定化、スパッタ発生量の低減化を図るよう
にしている。2. Description of the Related Art The applicant of the present invention has proposed that a flux cored wire used in gas shielded arc welding using carbon dioxide gas or a mixed gas of carbon dioxide gas and argon as a shielding gas to stabilize the arc by stabilizing the arc. In order to reduce the generation amount, BaF 2 as fluoride in the flux
A barium fluoride-based flux-cored wire to which is added is proposed (Japanese Patent No. 2758483). In this barium fluoride flux cored wire, the wire is used as a negative electrode (base material: positive electrode) with a DC positive polarity in which DC arc welding is performed. In addition to the impact force of cations, high vapor pressure
Since a large reaction force due to evaporation of BaF 2 or the like acts, the droplet at the tip of the wire is impacted by these resultant forces, and becomes small droplets and smoothly transitions to the base material. Thus, the arc is stabilized and the amount of spatter generated is reduced.
【０００３】前記提案した従来のフラックス入りワイヤ
は、BaF2、Al、Mg、Fe、Mn及びSiを必須のフラックス成
分とし、これらのフラックス成分量を適正化することに
より、低溶接電流域（100 〜200 Ａ程度）においてスパ
ッタ発生量が少ないことを特長とするものである。The conventional flux-cored wire proposed above uses BaF 2 , Al, Mg, Fe, Mn and Si as essential flux components, and by optimizing the amount of these flux components, a low welding current range (100%) is obtained. (Approximately -200 A), the amount of spatter generation is small.
【０００４】[0004]
【発明が解決しようとする課題】しかし前記従来のフラ
ックス入りワイヤでは、重力の影響によって溶融金属が
垂れ下がり易い立向き・上向き溶接などでの溶接性（良
好なビード形状の得られ易さ）が十分でなく、また、溶
接金属の靱性も満足できるものでなかった。However, the conventional flux-cored wire has sufficient weldability (easy to obtain a good bead shape) in vertical / upward welding where the molten metal tends to sag due to the effect of gravity. In addition, the toughness of the weld metal was not satisfactory.
【０００５】本発明の目的は、直流正極性での炭酸ガス
アーク溶接で使用されるフラックス入りワイヤであっ
て、低電流から中電流の溶接電流範囲（70〜300 Ａ程
度）においてスパッタ発生量が少なく、かつ、靱性の良
好な溶接金属が得られ、また、下向き溶接のみならず立
向き・上向き溶接などの全姿勢での溶接性が良好な直流
正極性用炭酸ガスアーク溶接フラックス入りワイヤを提
供することにある。また、本発明の他の目的は、該フラ
ックス入りワイヤを用いることにより、スパッタ発生量
が少なく、かつ耐気孔性に優れた溶接を行うことができ
る亜鉛めっき鋼板の溶接方法を提供することにある。An object of the present invention is to provide a flux-cored wire for use in carbon dioxide arc welding with a DC positive polarity, which has a small amount of spatter in a welding current range of low to medium current (about 70 to 300 A). To provide a carbon dioxide gas arc welding flux cored wire for DC positive polarity, which provides a weld metal having good toughness and good weldability not only in downward welding but also in all postures such as vertical and upward welding. It is in. Another object of the present invention is to provide a method for welding a galvanized steel sheet, which uses the flux-cored wire to generate a small amount of spatter and perform welding with excellent porosity resistance. .
【０００６】[0006]
【課題を解決するための手段】請求項１の発明に係る直
流正極性用炭酸ガスアーク溶接フラックス入りワイヤ
は、鋼製外皮内にフラックスを充填してなり、直流正極
性で使用される炭酸ガスアーク溶接フラックス入りワイ
ヤにおいて、フラックス成分として、ワイヤ全重量に対
する重量％で、Al：2 〜3.5 重量％、Mg：0.1 〜0.9 重
量％、BaF2：1 〜5 重量％及びZr：0.01〜1 重量％を含
有し、ワイヤ全重量に対するフラックス充填率が5 〜30
重量％であることを特徴とするものである。The flux-cored wire for carbon dioxide arc welding for direct current positive polarity according to the invention of claim 1 is formed by filling a steel sheath with a flux and used for direct current positive polarity carbon dioxide arc welding. in flux-cored wire, as the flux component, by weight relative to the total wire weight, Al: 2 to 3.5 wt%, Mg: 0.1 to 0.9 wt%, BaF 2: 1 to 5 wt% and Zr: 0.01 to 1% by weight Contains, flux filling rate of 5 to 30 with respect to the total weight of the wire
% By weight.
【０００７】請求項２の発明は、前記請求項１記載の直
流正極性用炭酸ガスアーク溶接フラックス入りワイヤに
おいて、ワイヤ全重量に対する重量％で、鋼製外皮及び
フラックス中のMnの総和：1 〜2.5 重量％、鋼製外皮及
びフラックス中のSiの総和：0.02〜0.6 重量％、鋼製外
皮及びフラックス中のC の総和：0.08重量％以下である
ことを特徴とするものである。請求項３の発明は、前記
請求項１又は２に記載の直流正極性用炭酸ガスアーク溶
接フラックス入りワイヤにおいて、ワイヤ全重量に対す
る重量％で、鋼製外皮及びフラックス中のP の総和：0.
015 〜0.05重量％であることを特徴とするものである。
請求項４の発明は、前記請求項１〜３のいずれか１項に
記載の直流正極性用炭酸ガスアーク溶接フラックス入り
ワイヤにおいて、フラックス中にワイヤ全重量に対する
重量％で、Niを0.1 〜3 重量％含有することを特徴とす
るものである。According to a second aspect of the present invention, there is provided the carbon dioxide arc welding flux cored wire for direct current positive polarity according to the first aspect, wherein the total of Mn in the steel sheath and the flux is 1 to 2.5% by weight based on the total weight of the wire. % By weight, the total of Si in the steel shell and the flux: 0.02 to 0.6% by weight, and the total of C in the steel shell and the flux: 0.08% by weight or less. According to a third aspect of the present invention, there is provided the carbon dioxide arc welding flux cored wire for direct current positive polarity according to the first or second aspect, wherein the sum of P in the steel sheath and the flux is 0.
015 to 0.05% by weight.
According to a fourth aspect of the present invention, there is provided the carbon dioxide arc welding flux cored wire for direct current positive polarity according to any one of the first to third aspects, wherein the flux contains Ni in an amount of 0.1 to 3% by weight based on the total weight of the wire. %.
【０００８】また、請求項５の発明に係る亜鉛めっき鋼
板の溶接方法は、前記請求項１〜４のいずれか１項に記
載の直流正極性用炭酸ガスアーク溶接フラックス入りワ
イヤを用いて、亜鉛めっき鋼板（表面に亜鉛又は亜鉛を
含む合金をめっき処理した鋼板）の溶接を行うものであ
る。According to a fifth aspect of the present invention, there is provided a method for welding a galvanized steel sheet, comprising the step of using the flux-cored wire for carbon dioxide arc welding for direct current positive polarity according to any one of the first to fourth aspects. This is for welding a steel plate (a steel plate having a surface plated with zinc or an alloy containing zinc).
【０００９】前記の特徴を有する本願発明に係る直流正
極性用炭酸ガスアーク溶接フラックス入りワイヤによる
と、低電流から中電流の溶接電流範囲（70〜300 Ａ程
度）においてスパッタ発生量が少なく、かつ、靱性の良
好な溶接金属が得られ、また、全姿勢での溶接性（良好
なビード形状の得られ易さ）が良い。また、本願発明の
ワイヤを用いた亜鉛めっき鋼板の炭酸ガスアーク溶接
は、亜鉛めっき鋼板の溶接で重要である耐気孔性、スパ
ッタ低減化に優れている。According to the carbon dioxide arc welding flux cored wire for DC positive polarity according to the present invention having the above characteristics, the amount of spatters generated is small in a welding current range from low current to medium current (about 70 to 300 A), and A weld metal with good toughness can be obtained, and good weldability (easy bead shape can be obtained) in all positions. Carbon dioxide arc welding of a galvanized steel sheet using the wire of the present invention is excellent in porosity resistance and spatter reduction which are important in welding a galvanized steel sheet.
【００１０】[0010]
【発明の実施の形態】本願発明に係るフラックス入りワ
イヤでは、主にAl、Mg、Zr、BaF2などのフラックス成分
量を適正にバランス化することにより、低電流から中電
流の溶接電流範囲（70〜300 Ａ程度）においてスパッタ
発生量が少なく、また、全姿勢で良好なビード形状が得
られるようにしたものである。すなわち、Al，Mgという
強力な脱酸剤は、溶融金属中の酸素量を低減させて溶融
金属の粘性を高めることにより、立向き溶接などで重力
の影響に抗して良好な形状のビードが得られる役割を担
う。また、Zrは、炭酸ガスアーク溶接においてAl，Mgを
添加した上でさらに酸素量を低減させ溶融金属の粘性を
より高める役割を担うことが判明した。フッ化物である
BaF2は、直流正極性でアークを安定にすることでスパッ
タ発生量を減らすアーク安定剤であるとともに、溶接金
属中の酸素量を上昇させることなくビード形状を整える
スラグ形成剤の役割を担う。さらに炭酸ガスアーク溶接
において、フェライト形成元素であるAl，Si、及びオー
ステナイト形成元素であるNi，Mn，C の成分量を適正化
することにより、靱性の良好な溶接金属が得られる。BEST MODE FOR CARRYING OUT THE INVENTION In the flux cored wire according to the present invention, the amount of flux components such as Al, Mg, Zr, and BaF 2 is appropriately balanced, so that the welding current range from low to medium current ( (Approximately 70 to 300 A), the amount of spatter is small, and a good bead shape can be obtained in all postures. In other words, strong deoxidizers such as Al and Mg reduce the amount of oxygen in the molten metal and increase the viscosity of the molten metal, so that a bead with a good shape can be formed against the influence of gravity, such as in vertical welding. Take the role that can be obtained. In addition, it was found that Zr plays a role in further increasing the viscosity of the molten metal by further reducing the amount of oxygen after adding Al and Mg in carbon dioxide gas arc welding. Is fluoride
BaF 2 is an arc stabilizer that reduces the amount of spatter generated by stabilizing the arc with DC positive polarity, and also plays a role of a slag forming agent that adjusts the bead shape without increasing the amount of oxygen in the weld metal. Further, in carbon dioxide gas arc welding, a weld metal having good toughness can be obtained by optimizing the component amounts of the ferrite-forming elements Al and Si and the austenite-forming elements Ni, Mn and C.
【００１１】本願発明に係るフラックス入りワイヤで
は、前述のように溶融金属がその粘性が高く垂れ下がり
難いことから、下向き・立向き溶接などにおいて、ルー
トギャップ（開先ルート間隙）を有する突合せ継手を、
従来と違って裏当て材（ビードの垂れ落ちを防いで裏ビ
ードを形成するためのもの）を用いることなく、裏ビー
ドを形成し片面溶接することも可能である。In the flux-cored wire according to the present invention, as described above, since the molten metal has a high viscosity and is unlikely to hang down, a butt joint having a root gap (a groove root gap) in downward / vertical welding is used.
Unlike the conventional method, it is also possible to form a back bead and perform one-side welding without using a backing material (for forming a back bead while preventing the bead from dripping).
【００１２】ところで、周知のように、亜鉛めっき鋼板
のアーク溶接では、アーク熱による亜鉛蒸気によりピッ
ト（溶接金属の表面に現れた気孔）やブローホール（溶
接金属の内部に存在する気孔）等の気孔が多発し、ま
た、亜鉛蒸気の影響によりアークが乱れてスパッタ発生
量が多いということが知られており、耐気孔性の向上と
スパッタの低減化を図る必要がある。本願発明のワイヤ
は亜鉛めっき鋼板の溶接においても耐気孔性、スパッタ
低減化に優れている。すなわち、Al，Mg，Zrは、溶融金
属の粘性を高めて溶融金属中での亜鉛蒸気の成長を抑制
する。また、P の適量添加によって該P と亜鉛との化合
物を形成し、これにより溶融した亜鉛が蒸気化するのを
抑制し、さらに、BaF2の適量添加によって溶滴移行及び
溶融池を安定化し、これによりアークが安定してスパッ
タの発生量は少ない。特に、どぶ漬けの亜鉛めっき鋼板
のように亜鉛目付量が５５０ｇ／ｍ2 程度と多い亜鉛め
っき鋼板の場合、P を適量含有させた本願ワイヤによる
溶接では耐気孔性が良い。By the way, as is well known, in arc welding of galvanized steel sheet, pits (pores appearing on the surface of the weld metal) and blow holes (pores existing inside the weld metal) due to zinc vapor due to arc heat are generated. It is known that a large number of pores are generated, and that the arc is disturbed by the effect of zinc vapor, resulting in a large amount of spatter. Therefore, it is necessary to improve porosity resistance and reduce spatter. The wire of the present invention is excellent in porosity resistance and spatter reduction even in welding galvanized steel sheets. That is, Al, Mg, and Zr increase the viscosity of the molten metal and suppress the growth of zinc vapor in the molten metal. In addition, the addition of an appropriate amount of P forms a compound of the P and zinc, thereby suppressing the vaporization of the molten zinc, and further stabilizing the droplet transfer and the molten pool by adding an appropriate amount of BaF 2 , This stabilizes the arc and reduces the amount of spatter generated. In particular, in the case of a galvanized steel sheet having a large weight per unit area of about 550 g / m 2 , such as a galvanized steel sheet which is pickled, welding with the present wire containing an appropriate amount of P has good porosity resistance.
【００１３】以下に、本願発明に係るワイヤを前記した
構成に限定した理由を説明する。なお、各成分の含有量
はワイヤ全重量に対する重量％である。The reason why the wire according to the present invention is limited to the above-described configuration will be described below. The content of each component is% by weight based on the total weight of the wire.
【００１４】Alは、フラックス中に必須として入れる成
分であって、強力な脱酸剤で溶融金属の粘性を高めて全
姿勢溶接でのビード形状を良くするとともに、直流正極
性でのアークを安定にする効果がある。しかし、2 重量
％未満ではアークが不安定でスパッタの発生量も多く、
一方、3.5 重量％を超えると溶接金属中のAl量が過剰と
なり、溶接金属の組織が粗大化し、靱性が低下する。し
たがって、Al量は2 〜3.5 重量％の範囲とする。Alは、
金属Alの形態でもよいし、Fe−Al，Al−Mg等の合金形態
で添加してもよい。Al is an essential component to be added to the flux. A powerful deoxidizer increases the viscosity of the molten metal to improve the bead shape in all-position welding and stabilizes the arc with DC positive polarity. Has the effect of However, if it is less than 2% by weight, the arc is unstable and the amount of spatter generated is large,
On the other hand, if it exceeds 3.5% by weight, the amount of Al in the weld metal becomes excessive, the structure of the weld metal becomes coarse, and the toughness decreases. Therefore, the Al content is in the range of 2 to 3.5% by weight. Al is
It may be added in the form of metal Al or in the form of an alloy such as Fe-Al or Al-Mg.
【００１５】Mgは、フラックス中に必須として入れる成
分であって、強力な脱酸剤で溶融金属の粘性を高めて全
姿勢溶接でのビード形状を良好にするとともに、直流正
極性でのアークを安定にする効果がある。しかし、0.1
重量％未満ではアークが不安定でスパッタの発生量も多
く、一方、0.9 重量％を超えるとアークの集中性が劣
り、これによってスパッタが増大する。したがって、Mg
量は0.1 〜0.9 重量％の範囲とする。Mgの添加形態とし
ては、金属Mg，Al−Mg等が挙げられる。なお、MgはAlと
似たような効果を担うものであるが、Alとの違いは、Al
よりも溶融金属の粘性を高める度合いが大きく、過剰添
加した場合、溶接金属の靱性の悪化には直接影響しない
ものの、スパッタが増大するとともにビード形状が凸ビ
ードとなって悪くなるという相違点がある。Mg is an essential component to be added to the flux. A strong deoxidizing agent increases the viscosity of the molten metal to improve the bead shape in all-position welding, and reduces the arc of DC positive polarity. It has the effect of stabilizing. But 0.1
If it is less than 0.9% by weight, the arc is unstable and a large amount of spatter is generated. Therefore, Mg
The amount ranges from 0.1 to 0.9% by weight. Examples of the addition form of Mg include metal Mg, Al-Mg, and the like. Although Mg has a similar effect to Al, the difference from Al is Al.
The degree of increasing the viscosity of the molten metal is greater than that, and if added excessively, it does not directly affect the deterioration of the toughness of the weld metal, but there is a difference that spatter increases and the bead shape becomes a convex bead and worsens. .
【００１６】BaF2は、フラックス中に必須として入れる
成分であって、直流正極性でアークを安定にしてスパッ
タ発生量を減らす効果がある。しかし、BaF2量が1 重量
％未満ではそのような効果が発揮されず、一方、5 重量
％を超えるとワイヤ先端の溶滴が大粒化してスムーズな
溶滴移行を行わず逆にスパッタが大粒化しスパッタ発生
量が増加する。したがって、BaF2量は1 〜5 重量％（Ba
換算値：0.8 〜4 重量％）の範囲とする。なお、他のフ
ッ化物、例えばSrF2，CaF2，LiF ，MgF2，NaF，K2SiF6
等のフッ化物も、スラグ形成剤としての観点から必要に
応じて添加可能であるが、これらをBaF2よりも多く添加
することは、アーク安定性の点から好ましくない。BaF 2 is a component that is essentially contained in the flux, and has the effect of reducing the amount of spatter generated by stabilizing the arc with a DC positive polarity. However, when the amount of BaF 2 is less than 1% by weight, such an effect is not exerted. On the other hand, when the amount of BaF 2 exceeds 5% by weight, droplets at the wire tip become large, and smooth droplet transfer is not performed. And the amount of spatter generated increases. Therefore, the amount of BaF 2 is 1 to 5% by weight (Ba
(Converted value: 0.8 to 4% by weight). In addition, other fluorides, for example, SrF 2 , CaF 2 , LiF, MgF 2 , NaF, K 2 SiF 6
Can be added as necessary from the viewpoint of a slag forming agent, but adding more than BaF 2 is not preferable from the viewpoint of arc stability.
【００１７】Zrは、フラックス中に必須として入れる成
分であって、強力な脱酸剤で溶融金属の粘性を高めて全
姿勢溶接での溶接性（良好なビード形状の得られ易さ）
を良くするとともに、アークを安定にする効果がある。
特に、炭酸ガスアーク溶接においてAl，Mgを添加した上
でさらに溶融金属の酸素量を低減させ粘性をより高める
場合に有効である。しかし、0.01重量％未満では全姿勢
での溶接性向上効果が発揮されず、かつ、スパッタ発生
量が増大し、一方、1 重量％を超えると溶接金属の靱性
が悪化する。したがって、Zr量は0.01〜1 重量％の範囲
とする。Zrの添加形態としては、Fe−Zr，Fe−Si−Zrが
挙げられる。Zr is an essential component to be added to the flux, and increases the viscosity of the molten metal with a strong deoxidizing agent to make it weldable in all-position welding (easy to obtain a good bead shape).
And the effect of stabilizing the arc.
This is particularly effective in carbon dioxide arc welding when Al and Mg are added and the oxygen content of the molten metal is further reduced to further increase the viscosity. However, if the content is less than 0.01% by weight, the effect of improving the weldability in all positions is not exhibited, and the amount of spatters increases, while if it exceeds 1% by weight, the toughness of the weld metal deteriorates. Therefore, the Zr content is in the range of 0.01 to 1% by weight. Examples of the addition form of Zr include Fe-Zr and Fe-Si-Zr.
【００１８】Mnは、オーステナイト形成元素であり、Al
を含んだ溶接金属での靱性を確保するのに有効な成分で
ある。しかし、鋼製外皮及びフラックス中のMnの総和
（T.Mn）が1 重量％未満ではそのような効果が十分発揮
されず、一方、2.5 重量％を超えると溶接金属の強度が
高くなりすぎて逆に靱性が低下する。したがって、Mn量
（T.Mn）は1 〜2.5 重量％の範囲がよい。Mnは、鋼製外
皮Mnとの総和で規定し、フラックスからは、金属Mnの形
態の他、Fe−Mn，Fe−Si−Mn等の合金形態で添加でき
る。Mn is an austenite-forming element, and Al
It is an effective component for ensuring the toughness of the weld metal containing. However, if the total amount of Mn (T.Mn) in the steel shell and flux is less than 1% by weight, such effects are not sufficiently exhibited, while when it exceeds 2.5% by weight, the strength of the weld metal becomes too high. Conversely, the toughness decreases. Therefore, the amount of Mn (T.Mn) is preferably in the range of 1 to 2.5% by weight. Mn is defined by the total sum with the steel sheath Mn. From the flux, it can be added in the form of metal Mn or in the form of an alloy such as Fe-Mn or Fe-Si-Mn.
【００１９】Siは、フェライト形成元素であり、母材と
溶接金属とのなじみ、いわゆるビードのなじみを良くす
るのに有効な成分である。しかし、鋼製外皮及びフラッ
クス中のSiの総和（T.Si）が0.02重量％未満ではそのよ
うな効果が十分発揮されず、一方、0.6 重量％を超える
と溶接金属の靱性が低下する。したがって、Si量（T.S
i）は0.02〜0.6 重量％の範囲がよい。Siは、鋼製外皮S
iとの総和で規定し、フラックスからは、Fe−Si，Fe−S
i−Zr等の合金形態で添加できる。Si is a ferrite-forming element and is an effective component for improving the compatibility between the base material and the weld metal, that is, the so-called bead. However, if the total amount of Si (T.Si) in the steel shell and the flux is less than 0.02% by weight, such an effect is not sufficiently exhibited, while when it exceeds 0.6% by weight, the toughness of the weld metal decreases. Therefore, the amount of Si (TS
i) is preferably in the range of 0.02 to 0.6% by weight. Si is steel sheath S
It is defined by the sum with i. From the flux, Fe-Si, Fe-S
It can be added in the form of an alloy such as i-Zr.
【００２０】C は、オーステナイト形成元素であり、Al
を含んだ溶接金属での靱性を確保するのに有効な成分で
ある。しかし、鋼製外皮及びフラックス中のC の総和
（T.C）が0.08重量％を超えると、溶接金属の強度が高
くなりすぎて逆に靱性が低下する。よって、C 量（T.C
）は0.08重量％以下がよい。通常、C は鋼製外皮に含
まれている。C is an austenite forming element;
It is an effective component for ensuring the toughness of the weld metal containing. However, when the total C (TC) in the steel shell and the flux exceeds 0.08% by weight, the strength of the weld metal becomes too high, and conversely, the toughness decreases. Therefore, the amount of C (TC
) Is preferably 0.08% by weight or less. Usually, C is contained in the steel shell.
【００２１】P は、亜鉛との安定な化合物（P −Zn系、
P −Zn−Fe系）を生成し、これにより亜鉛蒸気の発生量
を減少させ、気孔（ピット、ブローホール）の発生を抑
制する効果がある。P の量は鋼製外皮及びフラックス中
の総和（T.P ）で規定し、P量が0.015 重量％未満では
そのような効果が十分発揮されず、一方、0.05重量％を
超えると、溶融金属の最終凝固域に濃縮されるP 量が多
くなるため、溶接割れ（特に高温割れ）の発生に対する
感受性が高くなり、溶接条件・施工条件によっては溶接
割れが発生することがある。よって、P 量（T.P ）は0.
015 〜0.05重量％の範囲がよい。通常、P は鋼製外皮に
も含まれており、フラックスからは、Fe−P 等の形態で
添加できる。P is a stable compound with zinc (P-Zn system,
(P-Zn-Fe system), which has the effect of reducing the amount of zinc vapor generated and suppressing the generation of pores (pits, blow holes). The amount of P is defined by the total (TP) in the steel shell and the flux. If the P content is less than 0.015% by weight, such effects are not sufficiently exerted. Since the amount of P concentrated in the solidification zone increases, the susceptibility to the occurrence of welding cracks (particularly high-temperature cracking) increases, and welding cracks may occur depending on welding conditions and construction conditions. Therefore, the amount of P (TP) is 0.
The range is preferably from 015 to 0.05% by weight. Normally, P is also contained in the steel sheath and can be added in the form of Fe-P or the like from the flux.
【００２２】Niは、オーステナイト形成元素で比較的高
価であるものの、Mn，C のように、Alを含んだ溶接金属
での靱性を確保するために有効な成分である。しかし、
Ni量が0.1 重量％未満ではそのような効果が十分発揮さ
れず、一方、3 重量％を超えると溶接金属の強度が高く
なりすぎて逆に靱性が低下する。したがって、Ni量は0.
1 〜3 重量％の範囲がよい。Niは、金属Niなどの形態で
フラックスから添加する。Ni is an austenite-forming element which is relatively expensive, but is an effective component for securing toughness in a weld metal containing Al, such as Mn and C. But,
If the Ni content is less than 0.1% by weight, such an effect is not sufficiently exhibited, while if it exceeds 3% by weight, the strength of the weld metal becomes too high, and conversely, the toughness decreases. Therefore, the Ni content is 0.
A range of 1 to 3% by weight is good. Ni is added from the flux in the form of metallic Ni or the like.
【００２３】ワイヤ全重量に対するフラックス充填率は
5 〜30重量％の範囲にする。すなわち、フラックス充填
率が5 重量％未満ではフラックス構成成分の個々の含有
量が不足するために満足な効果を得ることができず、一
方、30重量％を超えると鋼製外皮を薄肉としなければな
らず、ワイヤへの溶接電流密度が高くなりすぎてアーク
が不安定となり、スパッタ発生量が増大する。したがっ
て、フラックス充填率は5 〜30重量％の範囲とし、各フ
ラックス成分の有効発揮及びアークの安定化の点より、
7 〜20重量％の範囲がより好ましい。The flux filling rate with respect to the total weight of the wire is
It should be in the range of 5 to 30% by weight. In other words, if the flux filling rate is less than 5% by weight, satisfactory effects cannot be obtained due to insufficient individual components of the flux components. On the other hand, if the flux filling rate exceeds 30% by weight, the steel shell must be thinned. Instead, the welding current density to the wire becomes too high, the arc becomes unstable, and the amount of spatter generated increases. Therefore, the flux filling rate is set in the range of 5 to 30% by weight, and from the viewpoint of effective use of each flux component and stabilization of the arc,
A range of 7 to 20% by weight is more preferred.
【００２４】その他、本発明のワイヤでは、Al，Mg，Zr
以外の強力な脱酸剤として、Ca，Tiなどを脱酸の目的
で、フラックス又は／及び鋼製外皮に含有させてもよ
い。また、低温での靱性を確保するため、フラックス又
は／及び鋼製外皮に、Ti又は／及びB を含有させてもよ
い。また、ビード形状を良好にすべくスラグ形成剤とし
て種々の酸化物をフラックス中に添加可能ではあるが、
これによりスパッタ発生量が増える傾向がある。なお、
鉄酸化物やMn酸化物のような中性系酸化物、及び、Mg酸
化物やAl酸化物のような塩基性酸化物は、スパッタの増
大度合いが比較的少ない酸化物である。In addition, in the wire of the present invention, Al, Mg, Zr
As a strong deoxidizing agent other than the above, Ca, Ti, or the like may be contained in the flux or / and the steel sheath for the purpose of deoxidizing. Further, in order to ensure toughness at low temperature, Ti or / and / or B may be contained in the flux or / and the steel sheath. Although various oxides can be added to the flux as a slag forming agent to improve the bead shape,
This tends to increase the amount of spatter generated. In addition,
Neutral oxides such as iron oxides and Mn oxides, and basic oxides such as Mg oxides and Al oxides are oxides with relatively little increase in spatter.
【００２５】ワイヤ断面形状については、例えば図１
（ａ）〜（ｄ）に例示する種々の形状のものが採用でき
る。図１（ｄ）の形状（継目無し）の場合にはワイヤ表
面に銅めっきを施しても構わない。For the wire cross-sectional shape, see FIG.
Various shapes illustrated in (a) to (d) can be adopted. In the case of the shape shown in FIG. 1D (seamless), copper plating may be applied to the surface of the wire.
【００２６】[0026]
【実施例】表２に示す化学成分の鋼製外皮（JIS G 3141
SPCC-SD相当）を用いて、表３及び表４に示すフラック
ス入りワイヤを製作した。なお、表３及び表４における
ｗｔ％はワイヤ全重量に対する重量％である。また、各
ワイヤはいずれも、ワイヤ径：φ1.4 ｍｍ、フラックス
充填率：15重量％であり、ワイヤ断面形状は図１（ｂ）
である。[Examples] Steel skins (JIS G 3141) having the chemical components shown in Table 2
Using SPCC-SD), the flux-cored wires shown in Tables 3 and 4 were produced. In Tables 3 and 4, wt% is a percentage by weight based on the total weight of the wire. Each wire has a wire diameter of 1.4 mm and a flux filling rate of 15% by weight.
It is.
【００２７】これらのフラックス入りワイヤを用いて、
表１に示す溶接試験条件で、全姿勢溶接の代表として立
向き姿勢の多層多パス溶接をＶ形突合せ継手にて実施
し、良好なビード形状の得られ易さ（溶接性）、スパッ
タ発生の度合い、溶接金属の靱性（JIS Z 3313に準じ
る）について評価した。Using these flux-cored wires,
Under the welding test conditions shown in Table 1, multi-pass multi-pass welding in a vertical position was carried out with a V-shaped butt joint as a representative of all position welding, and it was easy to obtain a good bead shape (weldability) and spatter generation. The degree and toughness of the weld metal (according to JIS Z 3313) were evaluated.
【００２８】[0028]
【表１】 [Table 1]
【００２９】[0029]
【表２】 [Table 2]
【００３０】[0030]
【表３】 [Table 3]
【００３１】[0031]
【表４】 [Table 4]
【００３２】[0032]
【表５】 [Table 5]
【００３３】溶接試験結果を表５に示す。評価は、◎：
特に良好、○：良好、△：やや劣る、×：劣る、とし
た。Table 5 shows the results of the welding test. Evaluation is ◎:
Particularly good, ：: good, Δ: slightly poor, ×: poor.
【００３４】試験結果から、No.1〜8 の比較例のワイヤ
では本発明で規定する要件の何れかを欠くため、次のよ
うな問題があった。No.1はAl量が下限値を下回るために
アーク不安定に起因してスパッタの発生量が多く、一
方、No.2は逆にAl量が上限値を外れて過剰となり、溶接
金属の靱性が低かった。No.3はMg量が下限値を下回るた
めにアークが不安定でスパッタ発生量が多く、一方、N
o.4は逆にMg量が上限値を上回るために凸ビード気味
で、また、スパッタが多発した。From the test results, the wires of Comparative Examples Nos. 1 to 8 lacked any of the requirements specified in the present invention, and thus had the following problems. No. 1 has a large amount of spatter due to arc instability because the Al content is below the lower limit, while No. 2 has an excessive Al content outside the upper limit and the toughness of the weld metal Was low. In No. 3, since the Mg amount was below the lower limit, the arc was unstable and the amount of spatter generated was large.
On the other hand, in the case of o.4, the Mg content exceeded the upper limit value, and the bead was slightly convex and spatter occurred frequently.
【００３５】No.5はBaF2量が下限値を下回るためにアー
クが不安定でスパッタ発生量が多く、No.6は逆にBaF2量
が上限値を上回るために大粒のスパッタが多発した。N
o.7はZrが下限値を下回るために溶融金属が垂れ下がり
気味でビード形状がやや悪く、かつ、アークがやや不安
定でスパッタ発生量がやや多かった。一方、No.8は逆に
Zrが上限値を上回るために溶接金属の靱性が低かった。In No. 5, the arc was unstable and the amount of spatter generated was large because the amount of BaF 2 was lower than the lower limit. On the contrary, in the case of No. 6, large spatter occurred frequently because the amount of BaF 2 exceeded the upper limit. . N
In o.7, since the Zr was below the lower limit, the molten metal tended to sag, the bead shape was slightly poor, the arc was slightly unstable, and the amount of spatter generated was somewhat large. On the other hand, No. 8
Since Zr exceeded the upper limit, the toughness of the weld metal was low.
【００３６】これに対し本発明例では、スパッタ発生量
が少なく、靱性の良好な溶接金属が得られており、しか
も、全姿勢溶接の代表である立向き姿勢の溶接において
も良好なビード形状が得られている。ただし、本発明例
（No.9〜No.22 ）において、T.Mnがその推奨範囲から外
れたNo.10 ，11、T.Siがその推奨範囲から外れたNo.13
、Ni量がその推奨範囲から外れたNo.17 、及び、T.C
がその推奨範囲から外れたNo.18 の発明例では、溶接金
属の靱性が△の評価であり、スラグ形成剤として酸化物
を付加したNo.21 ，22の発明例ではスパッタが△の評価
であった。On the other hand, in the example of the present invention, a weld metal having a small amount of spatter generation and good toughness is obtained, and a good bead shape can be obtained even in a vertical position welding which is a representative of all position welding. Have been obtained. However, in the examples of the present invention (No. 9 to No. 22), T.Mn was out of the recommended range, and No. 10, 11 and T.Si were out of the recommended range.
, No. 17 where the amount of Ni is out of the recommended range, and TC
However, the toughness of the weld metal was evaluated as △ in the No. 18 invention example out of the recommended range, and the spatter was evaluated as △ in the No. 21 and 22 invention examples in which an oxide was added as a slag forming agent. there were.
【００３７】次に、No.14 の発明例ワイヤと比較例ワイ
ヤとを用い、表６に示す溶接試験条件で亜鉛めっき鋼板
の炭酸ガスアーク溶接を実施した。Next, carbon dioxide arc welding of the galvanized steel sheet was performed under the welding test conditions shown in Table 6 using the No. 14 invention example wire and the comparative example wire.
【００３８】[0038]
【表６】 [Table 6]
【００３９】試験の結果、亜鉛めっき鋼板の炭酸ガスア
ーク溶接において、比較例ワイヤを用いた溶接では溶接
ビードにピット（気孔欠陥）が多発した。これに対し本
発明例のワイヤを用いた溶接では、ピットの発生はな
く、また、スパッタ発生量も少なかった。As a result of the test, in carbon dioxide arc welding of a galvanized steel sheet, pits (porous defects) frequently occurred in the weld bead in the welding using the comparative example wire. On the other hand, in the welding using the wire of the present invention, no pits were generated, and the amount of spatters generated was small.
【００４０】[0040]
【発明の効果】以上述べたように、本発明によれば、直
流正極性での炭酸ガスアーク溶接で使用されるフラック
ス入りワイヤであって、低電流から中電流の溶接電流範
囲（70〜300 Ａ程度）においてスパッタ発生量が少な
く、かつ、靱性の良好な溶接金属が得られ、また、下向
き溶接のみならず立向き・上向き溶接などの全姿勢での
溶接性が良好な直流正極性用炭酸ガスアーク溶接フラッ
クス入りワイヤを提供することができる。また、該ワイ
ヤを用いた亜鉛めっき鋼板の炭酸ガスアーク溶接による
と、ピットの発生がなく、スパッタ発生量が少ない溶接
を行うことができる。As described above, according to the present invention, there is provided a flux-cored wire for use in carbon dioxide arc welding with a DC positive polarity, which has a welding current range of low to medium current (70 to 300 A). ), A weld metal with low spatter generation and good toughness can be obtained, and a carbon dioxide gas arc for DC positive polarity with good weldability not only in downward welding but also in all postures such as vertical and upward welding. A welding flux cored wire can be provided. In addition, according to carbon dioxide arc welding of a galvanized steel sheet using the wire, pits are not generated, and welding with a small amount of spatter can be performed.
【図１】本願発明に係るフラックス入りワイヤの断面形
状の例を模式的に示す図である。FIG. 1 is a diagram schematically illustrating an example of a cross-sectional shape of a flux-cored wire according to the present invention.
Ｍ…鋼製外皮 Ｆ…フラックス M: steel skin F: flux
Claims (5)
り、直流正極性で使用される炭酸ガスアーク溶接フラッ
クス入りワイヤにおいて、フラックス成分として、ワイ
ヤ全重量に対する重量％で、Al：2 〜3.5 重量％、Mg：
0.1 〜0.9 重量％、BaF2：1 〜5 重量％及びZr：0.01〜
1 重量％を含有し、ワイヤ全重量に対するフラックス充
填率が5 〜30重量％であることを特徴とする直流正極性
用炭酸ガスアーク溶接フラックス入りワイヤ。1. A carbon dioxide arc welding flux-cored wire having a steel sheath filled with a flux and used for direct current positive polarity, wherein the flux component is Al: 2 to 3.5 weight% by weight based on the total weight of the wire. %, Mg:
0.1 to 0.9 wt%, BaF 2: 1 ~5 wt% and Zr: 0.01 to
A carbon dioxide arc welding flux cored wire for direct current positive polarity, comprising 1% by weight and a flux filling rate of 5 to 30% by weight based on the total weight of the wire.
皮及びフラックス中のMnの総和：1 〜2.5 重量％、鋼製
外皮及びフラックス中のSiの総和：0.02〜0.6 重量％、
鋼製外皮及びフラックス中のC の総和：0.08重量％以下
である請求項１記載の直流正極性用炭酸ガスアーク溶接
フラックス入りワイヤ。2. Sum of Mn in steel sheath and flux: 1 to 2.5 wt%, sum of Si in steel sheath and flux: 0.02 to 0.6 wt%, based on weight of total wire weight.
The carbon dioxide arc welding flux cored wire for direct current positive polarity according to claim 1, wherein the total of C 2 in the steel sheath and the flux is 0.08% by weight or less.
皮及びフラックス中のP の総和：0.015 〜0.05重量％で
ある請求項１又は２に記載の直流正極性用炭酸ガスアー
ク溶接フラックス入りワイヤ。3. The flux-cored carbon dioxide arc welding wire for DC positive polarity according to claim 1, wherein the total of P in the steel sheath and the flux is 0.015 to 0.05% by weight, based on the total weight of the wire.
量％で、Niを0.1 〜3 重量％含有する請求項１〜３のい
ずれか１項に記載の直流正極性用炭酸ガスアーク溶接フ
ラックス入りワイヤ。4. The flux-cored carbon dioxide arc welding wire for DC positive polarity according to claim 1, wherein the flux contains Ni in an amount of 0.1 to 3% by weight based on the total weight of the wire.
流正極性用炭酸ガスアーク溶接フラックス入りワイヤを
用いて、亜鉛めっき鋼板の溶接を行うことを特徴とする
亜鉛めっき鋼板の溶接方法。5. A method for welding a galvanized steel sheet, using the carbon dioxide arc welding flux-cored wire for direct current positive polarity according to any one of claims 1 to 4. .
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01265498A JP3513380B2 (en) | 1998-01-26 | 1998-01-26 | Carbon dioxide arc welding flux cored wire for DC positive polarity and welding method |
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP01265498A JP3513380B2 (en) | 1998-01-26 | 1998-01-26 | Carbon dioxide arc welding flux cored wire for DC positive polarity and welding method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH11207491A true JPH11207491A (en) | 1999-08-03 |
| JP3513380B2 JP3513380B2 (en) | 2004-03-31 |
Family
ID=11811360
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
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| JP (1) | JP3513380B2 (en) |
Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001353592A (en) * | 2000-04-13 | 2001-12-25 | Kawasaki Steel Corp | Steel wire for co2 gas shielded arc welding |
| JP2007098532A (en) * | 2005-10-06 | 2007-04-19 | Konyo:Kk | Hand tool and its manufacturing method |
| JP2015514584A (en) * | 2012-03-12 | 2015-05-21 | ホバート ブラザーズ カンパニー | System and method for welding electrodes |
| CN105189031A (en) * | 2013-03-13 | 2015-12-23 | 林肯环球股份有限公司 | Consumable for specially coated metals |
| WO2017013965A1 (en) * | 2015-07-17 | 2017-01-26 | 株式会社神戸製鋼所 | Wire containing flux for gas shield arc welding |
| WO2020226146A1 (en) | 2019-05-09 | 2020-11-12 | 株式会社神戸製鋼所 | Flux-cored wire, welding method, and weld metal |
| WO2020226148A1 (en) | 2019-05-09 | 2020-11-12 | 株式会社神戸製鋼所 | Flux-cored wire, welding method, and weld metal |
| EP3988240A4 (en) * | 2019-06-20 | 2023-07-19 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Flux-cored wire and welding method |
-
1998
- 1998-01-26 JP JP01265498A patent/JP3513380B2/en not_active Expired - Lifetime
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2001353592A (en) * | 2000-04-13 | 2001-12-25 | Kawasaki Steel Corp | Steel wire for co2 gas shielded arc welding |
| JP2007098532A (en) * | 2005-10-06 | 2007-04-19 | Konyo:Kk | Hand tool and its manufacturing method |
| JP2015514584A (en) * | 2012-03-12 | 2015-05-21 | ホバート ブラザーズ カンパニー | System and method for welding electrodes |
| US9950394B2 (en) | 2012-03-12 | 2018-04-24 | Hobart Brothers Company | Systems and methods for welding electrodes |
| CN105189031A (en) * | 2013-03-13 | 2015-12-23 | 林肯环球股份有限公司 | Consumable for specially coated metals |
| CN107848082A (en) * | 2015-07-17 | 2018-03-27 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
| JP2017024032A (en) * | 2015-07-17 | 2017-02-02 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding |
| WO2017013965A1 (en) * | 2015-07-17 | 2017-01-26 | 株式会社神戸製鋼所 | Wire containing flux for gas shield arc welding |
| CN107848082B (en) * | 2015-07-17 | 2020-09-04 | 株式会社神户制钢所 | Flux-cored wire for gas-shielded arc welding |
| WO2020226146A1 (en) | 2019-05-09 | 2020-11-12 | 株式会社神戸製鋼所 | Flux-cored wire, welding method, and weld metal |
| WO2020226148A1 (en) | 2019-05-09 | 2020-11-12 | 株式会社神戸製鋼所 | Flux-cored wire, welding method, and weld metal |
| KR20210145801A (en) | 2019-05-09 | 2021-12-02 | 가부시키가이샤 고베 세이코쇼 | Flux Cored Wire, Welding Method and Welding Metal |
| KR20210145800A (en) | 2019-05-09 | 2021-12-02 | 가부시키가이샤 고베 세이코쇼 | Flux Cored Wire, Welding Method and Welding Metal |
| EP3988240A4 (en) * | 2019-06-20 | 2023-07-19 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Flux-cored wire and welding method |
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| Publication number | Publication date |
|---|---|
| JP3513380B2 (en) | 2004-03-31 |
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