JP7260316B2 - High current density gas-shielded arc welding method - Google Patents
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本発明は、高電流密度ガスシールドアーク溶接方法に関し、鋼構造物のすみ肉溶接や開先内の１層または多層盛溶接をする場合において、高能率に溶接が可能で、溶接作業性及び溶接金属の機械的性能が優れた溶接金属を得ることができる高電流密度ガスシールドアーク溶接方法に関する。 The present invention relates to a high-current-density gas-shielded arc welding method, and when performing fillet welding of steel structures or single-layer or multi-layer welding in a groove, welding can be performed with high efficiency, and welding workability and welding are improved. The present invention relates to a high-current-density gas-shielded arc welding method capable of obtaining a weld metal having excellent metal mechanical properties.
近年、ガスシールドアーク溶接の自動化に伴い、更なる高能率化が要望されている。しかし、高能率化のために溶接電流を高くして溶接すると、スパッタ発生量が電流に比例して多くなり、溶接部の外観が損なわれるのでスパッタの除去が行われるが、スパッタの除去作業に時間を要してかえって溶接能率を低下させている。 In recent years, with the automation of gas-shielded arc welding, there has been a demand for even higher efficiency. However, when welding is performed with a high welding current for high efficiency, the amount of spatter generated increases in proportion to the current, and the appearance of the weld is damaged. It takes time and reduces the welding efficiency.
ガスシールドアーク溶接における溶接能率の向上技術は、例えば特許文献１において、Ｔｉ及びＳと電気比抵抗（ρ）を限定したソリッドワイヤを用いて高電流密度の溶接条件で溶接する高電流密度ガスシールドアーク溶接用鋼ワイヤの開示がある。しかし、特許文献１に記載のソリッドワイヤを用いて高電流密度の条件で溶接をした場合、アークが不安定となってスパッタ発生量が多くなり、その除去作業で溶接能率の向上は図れないという問題がある。 A technique for improving the welding efficiency in gas shielded arc welding is disclosed in, for example, Patent Document 1, in which a high current density gas shield is welded under high current density welding conditions using Ti and S and a solid wire with a limited electrical resistivity (ρ). There is a disclosure of steel wire for arc welding. However, when the solid wire described in Patent Document 1 is used for welding under conditions of high current density, the arc becomes unstable and a large amount of spatter is generated. There's a problem.
一方、フラックス入りワイヤを用いた高能率溶接は、特許文献２に、酸化物を１０％以下含むフラックス入りワイヤを用いて高電流密度の溶接をする技術の開示がある。しかし、特許文献２のフラックス入りワイヤは、ワイヤ中に酸化物を多く含むので溶接時にスラグ生成量が多くなり、多層盛溶接した場合スラグ巻き込み欠陥が生じやすく、また、ソリッドワイヤを用いた場合に比べるとスパッタ発生量は少ないものの除去作業低減の効果は少ない。さらに、ワイヤ中に酸化物を多く含むことと高電流密度条件で溶接するので溶接金属中の酸素量が多くなって溶接金属の靭性も低いという問題がある。 On the other hand, regarding high-efficiency welding using a flux-cored wire, Patent Document 2 discloses a technique of performing high-current-density welding using a flux-cored wire containing 10% or less of oxides. However, the flux-cored wire of Patent Document 2 contains a large amount of oxides in the wire, so the amount of slag generated during welding is large, and slag entrainment defects are likely to occur when multi-layer welding is performed. Although the amount of generated spatter is relatively small, the effect of reducing the removal work is small. Furthermore, since the wire contains a large amount of oxides and the welding is performed under high current density conditions, the amount of oxygen in the weld metal increases and the toughness of the weld metal is low.
また、特許文献３及び特許文献４にはフラックス入りワイヤを用いてパルスＭＡＧ溶接する技術の開示がある。特許文献３及び特許文献４は、金属粉を多量に含むメタル系フラックス入りワイヤを用いて、高溶着量を得るためにパルスピーク電流またはパルスベース電流を高くして、高溶着量を得ながらスパッタ発生量を低減するとしている。しかし、溶接電源が高価であることと、パルスピーク電流時にはワイヤ送給量が２０ｍ／ｍｉｎ以上の高速度で送給され、パルスベース電流時には１５ｍ／ｍｉｎ以下のワイヤ送給量となり、ワイヤ送給ローラの回転の緩急によってワイヤ送給ローラ部でワイヤがスリップしてアークが不安定となり細粒のスパッタ発生量が多く、ビード外観も不良となるという問題がある。また、高電流であるにもかかわらず開示されているフラックス入りワイヤの脱酸剤では溶接金属の靭性についての考慮がされていない。また、開示されているフラックス入りワイヤの酸化物では溶接止端部のなじみが悪くなりビード外観・形状が不良になるという問題もある。 Further, Patent Documents 3 and 4 disclose techniques for pulse MAG welding using a flux-cored wire. In Patent Documents 3 and 4, a metal flux-cored wire containing a large amount of metal powder is used, and the pulse peak current or pulse base current is increased in order to obtain a high amount of welding, and sputtering is performed while obtaining a high amount of welding. The company plans to reduce the amount of waste generated. However, the welding power source is expensive, and the wire feed rate is 20 m/min or more at the pulse peak current, and the wire feed rate is 15 m/min or less at the pulse base current. There is a problem that the wire slips on the wire feeding roller due to the speed of rotation of the roller, and the arc becomes unstable, resulting in a large amount of spatter of fine particles and a poor appearance of the bead. In addition, although the current is high, the disclosed flux-cored wire deoxidizing agent does not consider the toughness of the weld metal. In addition, the oxide of the disclosed flux-cored wire has a problem that the conformability of the weld toe is poor, resulting in poor bead appearance and shape.
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、ガスシールドアーク溶接用フラックス入りワイヤを用いた鋼構造物のすみ肉溶接や開先内の１層または多層盛溶接をする高電流密度ガスシールドアーク溶接方法において、スパッタ発生量が少なくビード外観・形状が良好であるなど溶接作業性に優れ、機械的性能にも優れた溶接金属を得ることができる高電流密度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。 Therefore, the present invention has been devised in view of the above-mentioned problems, and fillet welding of steel structures and single-layer or multi-layer welding in grooves using a flux-cored wire for gas-shielded arc welding. A high current density gas shield arc welding method that generates less spatter, has excellent welding workability such as good bead appearance and shape, and can obtain weld metal with excellent mechanical performance. An object of the present invention is to provide an arc welding method.
本発明者らは、上記問題点を解決するために、ガスシールドアーク溶接用フラックス入りワイヤを用いた高電流密度溶接において、アークが安定してスパッタ発生量が少なくビード外観・形状が良好で、溶接欠陥が生じず、高能率に強度及び靭性の良好な溶接金属を得るために、ガスシールドアーク溶接用フラックス入りワイヤの成分組成及び電流密度について詳細に検討した。 In order to solve the above problems, the present inventors have found that in high current density welding using a flux-cored wire for gas shielded arc welding, the arc is stable, the amount of spatter generated is small, and the bead appearance and shape are good. In order to efficiently obtain a weld metal with good strength and toughness without welding defects, the chemical composition and current density of a flux-cored wire for gas-shielded arc welding were investigated in detail.
その結果、高電流密度での溶接において、アークの安定性及びスパッタ発生量の低減は、ガスシールドアーク溶接用フラックス入りワイヤのＣ、Ａｌ、弗素化合物のＦ換算値の合計及びＮａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計を適量とするとともに過剰に電流密度を高くしないことによって達成できることを見出した。 As a result, in welding at high current densities, the stability of the arc and the reduction in the amount of spatter generated are the sum of the F conversion values of C, Al, and fluorine compounds in the flux-cored wire for gas-shielded arc welding, and the Na compounds and K compounds. It was found that the total amount of Na 2 O conversion value and K 2 O conversion value of is appropriate and the current density is not excessively increased.
ビード外観・形状は、ガスシールドアーク溶接用フラックス入りワイヤのＳｉＯ2の適正化で、スラグ剥離性はＳの適正化、耐溶接欠陥はＳｉＯ2合計及びＮａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計を適量とすることが有効であることを知見した。 The appearance and shape of the bead is determined by optimizing the SiO2 content of the flux-cored wire for gas-shielded arc welding, the slag removability is determined by optimizing the S content, and the weld defect resistance is determined by the total SiO2 and Na compound and K compound converted to Na2O . and the K 2 O conversion value are found to be effective.
また、高電流密度での溶接条件における溶接金属の適正な強度と靭性の向上をも同時に達成させるためには、ガスシールドアーク溶接用フラックス入りワイヤ中の酸化物を極力低減し、合金成分のＣ、Ｓｉ、Ｍｎ、Ｃｕ、Ｔｉ及びＡｌの含有量をそれぞれ適正化することが有効であることを知見した。特に、Ａｌを適量添加することによって、高電流密度溶接におけるＳｉ及びＭｎの酸化消耗を低減して溶接金属の強度の適正化及び靭性の向上に極めて効果があることを知見した。 In addition, in order to simultaneously achieve the appropriate strength and toughness improvement of the weld metal under welding conditions of high current density, oxides in the flux-cored wire for gas-shielded arc welding should be reduced as much as possible, and the alloy component C , Si, Mn, Cu, Ti and Al are found to be effective. In particular, it has been found that the addition of an appropriate amount of Al is extremely effective in reducing oxidation consumption of Si and Mn in high current density welding, optimizing the strength and improving the toughness of the weld metal.
さらに、靭性を低下させることなく高強度を得る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Ｎｉ、Ｃｒ及びＭｏの１種または２種以上をさらに適量含有させ、溶接金属の低温靭性を得るにはＢをさらに適量含有することが有効であることを知見した。 Furthermore, in order to obtain high strength without lowering the toughness, the flux-cored wire for gas-shielded arc welding further contains an appropriate amount of one or more of Ni, Cr and Mo to obtain low-temperature toughness of the weld metal. It has been found that it is effective to further contain an appropriate amount of B.
すなわち、本発明の要旨は、
（１）鋼製外皮にフラックスを充填してなるガスシールドアーク溶接用フラックス入りワイヤを電極として溶接を行う高電流密度ガスシールドアーク溶接方法において、ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの合計で、Ｃ：０．０３～０．１２％、Ｓｉ：０．２～１．０％、Ｍｎ：１．０～２．５％、Ｓ：０．０１～０．０３％、Ｃｕ：０．０５～０．４５％、Ｔｉ：０．０８～０．２０％、Ａｌ；０．０３～０．１５％を含有し、さらに、ワイヤ全質量に対する質量％で、フラックス中に、弗素化合物のＦ換算値の合計で０．０１～０．１０％、ＳｉＯ2：０．０１～０．２０％、Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計で０．０２～０．１５％を含有し、残部は鋼製外皮のＦｅ、鉄粉のＦｅ分、鉄合金粉のＦｅ分及び不可避不純物からなるガスシールドアーク溶接用フラックス入りワイヤを用い、電流密度が３２０～５２０Ａ／ｍｍ2の条件で溶接することを特徴する高電流密度ガスシールドアーク溶接方法。
That is, the gist of the present invention is
(1) In a high-current-density gas-shielded arc welding method in which a flux-cored wire for gas-shielded arc welding in which a steel sheath is filled with flux is used as an electrode for welding, the steel sheath and the flux are In total, C: 0.03 to 0.12%, Si: 0.2 to 1.0%, Mn: 1.0 to 2.5%, S: 0.01 to 0.03%, Cu: 0.05% to 0.45%, Ti: 0.08% to 0.20%, Al: 0.03% to 0.15%, and a fluorine compound in the flux in mass% relative to the total mass of the wire SiO 2 : 0.01 to 0.20%, the total of Na compound and K compound converted to Na 2 O and K 2 O converted to 0.01% to 0.10%. 02 to 0.15%, the balance being Fe in the steel skin, Fe content in the iron powder, Fe content in the iron alloy powder, and inevitable impurities. A high-current density gas-shielded arc welding method characterized by welding under conditions of up to 520 A/mm 2 .
（２）鋼製外皮とフラックスの合計で、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計を下記式で０．１５～０．６０をさらに含有する前記ガスシールドアーク溶接用フラックス入りワイヤにより溶接することを特徴とする（１）に記載の高電流密度ガスシールドアーク溶接方法。
［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］・・・・式
但し、［ ］は、各成分のワイヤ全質量に対する質量％を示す。
(2) The flux-cored wire for gas-shielded arc welding, which further contains 0.15 to 0.60 of the total of one or more of Ni, Cr and Mo in the total of the steel sheath and the flux according to the following formula. The high-current density gas-shielded arc welding method according to (1), wherein the welding is performed by
[Ni]/3+[Cr]+[Mo] Expression where [ ] indicates mass % of each component with respect to the total mass of the wire.
（３）ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの合計で、Ｂ：０．００１５～０．０１５０％をさらに含有する前記ガスシールドアーク溶接用フラックス入りワイヤにより溶接することを特徴とする（１）または（２）に記載の高電流密度ガスシールドアーク溶接方法。 (3) The flux-cored wire for gas-shielded arc welding further containing B: 0.0015 to 0.0150% in mass% relative to the total mass of the steel sheath and flux. The high-current density gas-shielded arc welding method according to (1) or (2).
（４）成形された前記鋼製外皮の合わせ目が溶接されていることで鋼製外皮に継目を無くした前記ガスシールドアーク溶接用フラックス入りワイヤにより溶接することを特徴とする（１）乃至（３）の何れかに記載の高電流密度ガスシールドアーク溶接方法にある。 (4) Welding is performed with the flux-cored wire for gas-shielded arc welding in which the seam of the formed steel skin is welded so that the steel skin is seamless (1) to ( 3) A high-current density gas-shielded arc welding method according to any one of 3) above.
本発明の高電流密度ガスシールドアーク溶接方法によれば、ガスシールドアーク溶接用フラックス入りワイヤを用いた鋼構造物のすみ肉溶接や開先内の１層または多層盛溶接をする高電流密度ガスシールドアーク溶接方法において、アークが安定してスパッタ発生量が少なくビード外観・形状が良好であるなど溶接作業性に優れ、溶接欠陥が無く、溶接金属の機械的性能にも優れるなど、高能率に高品質な溶接部を得ることができる。 According to the high-current-density gas-shielded arc welding method of the present invention, high-current-density gas welding for fillet welding of steel structures using a flux-cored wire for gas-shielded arc welding and single-layer or multi-layer fill welding in grooves is performed. In the shielded arc welding method, the arc is stable, the amount of spatter generated is small, and the appearance and shape of the bead are good, so the welding workability is excellent. High quality welds can be obtained.
まず、本発明の高電流密度ガスシールドアーク溶接方法の電流密度の限定理由を述べる。 First, the reasons for limiting the current density of the high-current-density gas-shielded arc welding method of the present invention will be described.
［電流密度：３２０～５２０Ａ／ｍｍ2］
本発明においては、鋼構造物の溶接を高能率に行うために高電流密度の溶接条件で実施する。電流密度が３２０Ａ／ｍｍ2未満であると、溶着量が少なく高能率に溶接することができない。一方、電流密度が５２０Ａ／ｍｍ2を超えると、後述するガスシールドアーク溶接用フラックス入りワイヤを用いてもスパッタ発生量が多くなる。したがって、電流密度は３２０～５２０Ａ／ｍｍ2とする。
[Current density: 320 to 520 A/mm 2 ]
In the present invention, welding of steel structures is performed under high current density welding conditions in order to perform welding with high efficiency. If the current density is less than 320 A/mm 2 , the amount of welding is small and efficient welding cannot be performed. On the other hand, if the current density exceeds 520 A/mm 2 , the amount of spatter generated increases even if a flux-cored wire for gas-shielded arc welding, which will be described later, is used. Therefore, the current density should be 320-520 A/mm 2 .
なお、本発明の高電流密度ガスシールドアーク溶接方法に用いるガスシールドアーク溶接用フラックス入りワイヤは、高電流密度で高溶着量を得ることからワイヤ径が１．２～１．６ｍｍであることが好ましい。 It should be noted that the flux-cored wire for gas-shielded arc welding used in the high-current-density gas-shielded arc welding method of the present invention has a wire diameter of 1.2 to 1.6 mm because a high amount of deposition is obtained at a high current density. preferable.
次いで、本発明の高電流密度ガスシールドアーク溶接方法に用いるガスシールドアーク溶接用フラックス入りワイヤは、各成分組成それぞれの単独及び共存による相乗効果によりなし得たもので、以下にそれぞれの各成分組成の限定理由を述べる。なお、各成分組成の含有量は、ガスシールドアーク溶接用フラックス入りワイヤ全質量に対する質量％で表すこととし、その質量％に関する記載を単に％として表すこととする。 Next, the flux-cored wire for gas-shielded arc welding used in the high-current-density gas-shielded arc welding method of the present invention was obtained by the synergistic effect of each component composition alone and coexistence. State the reason for the limitation. The content of each component composition is represented by mass% with respect to the total mass of the flux-cored wire for gas-shielded arc welding, and the description of the mass% is simply represented as %.
［鋼製外皮とフラックスの合計でＣ：０．０３～０．１２％］
Ｃは、溶接金属の強度を向上するために必要な元素である。Ｃが０．０３％未満であると、溶接金属の所望の強度が得られない。一方、Ｃが０．１２％を超えると、溶接金属の強度が高くなるとともに靭性が低下し、スパッタ発生量も多くなる。したがって、鋼製外皮とフラックスの合計でＣは０．０３～０．１２％とする。なお、Ｃは、鋼製外皮に含まれる成分の他、フラックスから金属粉及び合金粉等から添加できる。
[Total C of steel skin and flux: 0.03 to 0.12%]
C is an element necessary for improving the strength of the weld metal. If C is less than 0.03%, the desired strength of the weld metal cannot be obtained. On the other hand, when C exceeds 0.12%, the strength of the weld metal increases, the toughness decreases, and the amount of spatter generation increases. Therefore, the total C content of the steel skin and flux should be 0.03 to 0.12%. C can be added from metal powder, alloy powder, etc. from the flux, in addition to the components contained in the steel outer sheath.
「鋼製外皮とフラックスの合計でＳｉ：０．２～１．０％」
Ｓｉは、溶接金属の脱酸のために添加する。Ｓｉが０．２％未満であると、溶接金属の脱酸不足で靭性が低下する。またＳｉが０．２％未満であると、高電流密度の溶接においてはＳｉの消耗が大きいため溶接金属の強度も低くなる。一方、Ｓｉが１．０％を超えると、溶接金属の強度が高くなり靭性が低下する。したがって、鋼製外皮とフラックスの合計でＳｉは０．２～１．０％とする。なお、Ｓｉは、鋼製外皮に含まれる成分の他、フラックスから金属Ｓｉ、Ｆｅ－Ｓｉ、Ｆｅ－Ｓｉ－Ｍｎ等の合金粉から添加できる。
"Si: 0.2 to 1.0% in total of steel outer skin and flux"
Si is added for deoxidizing the weld metal. If the Si content is less than 0.2%, the deoxidation of the weld metal is insufficient, resulting in a decrease in toughness. Further, when the Si content is less than 0.2%, the strength of the weld metal is low due to large consumption of Si in high current density welding. On the other hand, when Si exceeds 1.0%, the strength of the weld metal increases and the toughness decreases. Therefore, the total Si content of the steel skin and the flux should be 0.2 to 1.0%. Si can be added from metal Si, Fe--Si, Fe--Si--Mn or other alloy powder from the flux, in addition to the components contained in the steel outer sheath.
［鋼製外皮とフラックスの合計でＭｎ：１．０～２．５％］
Ｍｎは、溶接金属の靭性確保と強度向上のために添加する。Ｍｎが１．０％未満であると、高電流密度の溶接においてはＭｎの消耗が大きいため溶接金属の強度が低く靭性が十分確保できなくなる。一方、Ｍｎが２．５％を超えると、溶接金属の強度が高くなり靭性が低下する。したがって、鋼製外皮とフラックスの合計でＭｎは１．０～２．５％とする。なお、Ｍｎは、鋼製外皮に含まれる成分の他、金属Ｍｎ、Ｆｅ－Ｍｎ、Ｆｅ－Ｓｉ－Ｍｎ等の合金粉から添加できる。
[Total Mn of steel skin and flux: 1.0 to 2.5%]
Mn is added to secure toughness and improve strength of the weld metal. If the Mn content is less than 1.0%, the consumption of Mn is large in welding at high current densities, so that the strength of the weld metal is low and sufficient toughness cannot be ensured. On the other hand, when Mn exceeds 2.5%, the strength of the weld metal increases and the toughness decreases. Therefore, Mn is set to 1.0 to 2.5% in total of the steel outer covering and the flux. Mn can be added from alloy powder such as metal Mn, Fe--Mn, Fe--Si--Mn, etc., in addition to components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＳ：０．０１～０．０３％］
本発明の高電流密度ガスシールドアーク溶接方法に用いるガスシールドアーク溶接用フラックス入りワイヤは、ワイヤ中の酸化物を極力低減しているが、高電流密度の溶接条件であるためにＳｉ、Ｍｎ、Ｔｉ及びＡｌの酸化消耗が大きいためスラグが生成され、多層盛溶接した場合に蓄積されたスラグの剥離性を向上するためにＳを添加する。Ｓが０．０１％未満であると、その効果が不十分で、特に多層盛溶接した場合にスラグ剥離性が不良となる。一方、Ｓが０．０３％を超えると、溶接金属に割れが生じるようになる。したがって、鋼製外皮とフラックスの合計でＳは０．０１～０．０３％とする。なお、Ｓは、鋼製外皮に含まれる成分の他、ＦｅＳ、鉄合金粉等から添加される。
[Total S of steel skin and flux: 0.01 to 0.03%]
The flux-cored wire for gas-shielded arc welding used in the high-current-density gas-shielded arc welding method of the present invention reduces oxides in the wire as much as possible. Slag is generated due to the large oxidation consumption of Ti and Al, and S is added to improve the releasability of accumulated slag when multi-layer welding is performed. If the S content is less than 0.01%, the effect is insufficient, and the slag removability becomes poor especially when multi-layer welding is performed. On the other hand, if S exceeds 0.03%, cracks will occur in the weld metal. Therefore, S is set to 0.01 to 0.03% in total of the steel skin and the flux. S is added from FeS, iron alloy powder, etc., in addition to components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＣｕ：０．０５～０．４５％］
Ｃｕは、溶接金属の組織を微細化して靭性を向上する効果がある。また、鋼製外皮の継目を無くして鋼製外皮表面にＣｕめっきを施すことによって、高電流密度の溶接でワイヤ送給速度が２０ｍ／ｍｉｎ以上となってもチップ磨耗を低減することができる。Ｃｕが０．０５％未満であると、溶接金属の靭性が低下する。また、鋼製外皮表面にＣｕめっきを施しても、非常に薄めっきとなりチップ磨耗抑制の効果が得られない。一方、Ｃｕが０．４５％を超えると、溶接金属に析出脆化が生じて靭性が低下する。したがって、鋼製外皮とフラックスの合計でＣｕは０．０５～０．４５％とする。なお、Ｃｕは、鋼製外皮に含まれる成分及び鋼製外皮表面に施したＣｕめっき分の他、フラックスからの金属Ｃｕ、Ｆｅ－Ｓｉ－Ｃｕ等の合金粉から添加できる。
[Cu: 0.05 to 0.45% in total of steel skin and flux]
Cu has the effect of refining the structure of the weld metal and improving toughness. In addition, by eliminating the joints of the steel skin and applying Cu plating to the surface of the steel skin, tip wear can be reduced even when the wire feed speed is 20 m/min or more in high current density welding. If Cu is less than 0.05%, the toughness of the weld metal is lowered. Also, even if Cu plating is applied to the surface of the steel outer skin, the plating is very thin and the effect of suppressing tip wear cannot be obtained. On the other hand, when Cu exceeds 0.45%, precipitation embrittlement occurs in the weld metal, resulting in a decrease in toughness. Therefore, the total content of Cu in the steel sheath and flux should be 0.05 to 0.45%. Cu can be added from metal Cu from flux, alloy powder such as Fe--Si--Cu, in addition to components contained in the steel skin and Cu plating applied to the surface of the steel skin.
［鋼製外皮とフラックスの合計でＴｉ：０．０８～０．２０％］
Ｔｉは、脱酸剤として作用するとともに、アークを安定にしてスパッタ発生量を抑制する効果がある。また、溶接金属中に微細酸化物を生成し溶接金属の靭性を向上させる。Ｔｉが０．０８％未満であると、アークが不安定になってスパッタ発生量が多くなり、また、溶接金属の靭性が低下する。一方、Ｔｉが０．２０％を超えると、溶接金属中に固溶Ｔｉが多くなって靭性が低下する。したがって、鋼製外皮とフラックスの合計でＴｉは０．０８～０．２０％とする。なお、Ｔｉは、鋼製外皮に含まれる成分の他、金属Ｔｉ、Ｆｅ－Ｔｉ等の合金粉から添加できる。
[Ti: 0.08 to 0.20% in total of steel skin and flux]
Ti acts as a deoxidizing agent and has the effect of stabilizing the arc and suppressing the amount of spatter generation. In addition, it forms fine oxides in the weld metal and improves the toughness of the weld metal. If Ti is less than 0.08%, the arc becomes unstable, the amount of spatter increases, and the toughness of the weld metal decreases. On the other hand, if Ti exceeds 0.20%, the amount of solid solution Ti increases in the weld metal, resulting in a decrease in toughness. Therefore, Ti is set to 0.08 to 0.20% in total of the steel outer covering and the flux. Incidentally, Ti can be added from metal Ti, alloy powder such as Fe—Ti, etc., in addition to components contained in the steel outer shell.
［鋼製外皮とフラックスの合計でＡｌ：０．０３～０．１５％］
Ａｌは、高電流密度の溶接において最も重要な脱酸剤である。Ａｌが０．０３％未満であると、前述のＳｉ及びＭｎの酸化消耗が多くなって、溶接金属の強度が低くなり靭性も低下する。一方、Ａｌが０．１５％を超えると、アークが不安定になってスパッタ発生量が多くなる。したがって、鋼製外皮とフラックスの合計でＡｌは０．０３～０．１５％とする。なお、Ａｌは、鋼製外皮に含まれる成分の他、金属Ａｌ、Ｆｅ－Ａｌ等の合金粉から添加できる。
[Al: 0.03 to 0.15% in total of steel skin and flux]
Al is the most important deoxidizing agent in high current density welding. If the Al content is less than 0.03%, the oxidation consumption of Si and Mn increases, and the strength and toughness of the weld metal decrease. On the other hand, if Al exceeds 0.15%, the arc becomes unstable and the amount of spatter generation increases. Therefore, Al is set to 0.03 to 0.15% in total of the steel skin and flux. In addition, Al can be added from metal Al, alloy powder such as Fe—Al, in addition to the components contained in the steel outer shell.
［フラックス中に含有する弗素化合物のＦ換算値の合計：０．０１～０．１０％］
弗素化合物は、アークを集中させて安定にする効果がある。弗素化合物のＦ換算値の合計が０．０１％未満であると、アークが集中せず不安定となってスパッタ発生量が多くなる。一方、弗素化合物のＦ換算値の合計が０．１０％を超えると、アークが荒くなりスパッタ発生量が多くなる。したがって、フラックス中の含有する弗素化合物のＦ換算値の合計は０．０１～０．１０％とする。なお、弗素化合物は、フラックスからの蛍石、弗化ソーダ、弗化カリ、弗化マグネシウム、珪弗化カリウム、氷晶石等から添加でき、Ｆ換算値はそれらに含有されるＦ量の合計である。
[Total F conversion value of fluorine compounds contained in flux: 0.01 to 0.10%]
The fluorine compound has the effect of concentrating and stabilizing the arc. If the total F-equivalent value of the fluorine compounds is less than 0.01%, the arc will not concentrate and become unstable, resulting in a large amount of spatter. On the other hand, if the total F conversion value of the fluorine compound exceeds 0.10%, the arc becomes rough and the amount of spatter generation increases. Therefore, the total F conversion value of the fluorine compounds contained in the flux should be 0.01 to 0.10%. The fluorine compound can be added from fluorite, sodium fluoride, potassium fluoride, magnesium fluoride, potassium silicofluoride, cryolite, etc. from the flux, and the F conversion value is the total amount of F contained in them. is.
［フラックス中に含有するＳｉＯ2：０．０１～０．２０％］
ＳｉＯ2は、高電流密度の溶接において少量添加することによってビード止端部のなじみを良好にしてビード外観・形状を良好にする効果がある。ＳｉＯ2が０．０１％未満であると、前記効果が得られずビード止端部のなじみが悪くなりビード外観・形状が不良になる。一方、ＳｉＯ2が０．２０％を超えると、多層盛溶接でスラグ生成量が多くなってスラグ巻き込み欠陥が生じやすくなる。またＳｉＯ2が０．２０％を超えると、溶接金属中の酸素量が多くなって靭性が低下する。したがって、フラックス中のＳｉＯ2は０．０１～０．２０％とする。なお、ＳｉＯ2は、フラックスからの珪砂、珪酸ソーダ、珪酸カリからなる水ガラスの固質成分等から添加できる。
[SiO 2 content in flux: 0.01 to 0.20%]
SiO 2 has the effect of improving the conformability of the bead toe and improving the appearance and shape of the bead by adding a small amount in high current density welding. If the SiO 2 content is less than 0.01%, the above effect cannot be obtained, and the conformability of the toe of the bead deteriorates, resulting in poor bead appearance and shape. On the other hand, if the SiO 2 content exceeds 0.20%, the amount of slag generated in multi-layer welding increases, and slag entrainment defects tend to occur. On the other hand, if the SiO 2 content exceeds 0.20%, the amount of oxygen in the weld metal increases and the toughness decreases. Therefore, SiO 2 in the flux should be 0.01 to 0.20%. SiO 2 can be added from silica sand from flux, sodium silicate, solid components of water glass made from potassium silicate, and the like.
［フラックス中に含有するＮａ化合物及びＫ化合物：Ｎａ2Ｏ換算値とＫ2Ｏ換算値の合計：０．０２～０．１５％］
Ｎａ化合物及びＫ化合物は、アークをソフトにして安定にする。Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計が０．０２％未満であると、前記効果が得られず、アークが不安定となってスパッタ発生量が多くなる。一方、Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計が０．１５％を超えると、多層盛溶接でスラグ生成量が多くなってスラグ巻き込み欠陥が生じやすくなる。また、ヒューム発生量が多くなる。したがって、フラックス中のＮａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計は０．０２～０．１５％とする。なお、Ｎａ化合物やＫ化合物は、フラックスから珪酸ソーダ及び珪酸カリからなる水ガラスの固質分、カリ長石、弗化ソーダ、珪弗化カリウム等の粉末から添加できる。
[Na compound and K compound contained in flux: total of Na 2 O conversion value and K 2 O conversion value: 0.02 to 0.15%]
Na compounds and K compounds soften and stabilize the arc. If the sum of the Na compound and K compound converted to Na 2 O and converted to K 2 O is less than 0.02%, the above effect cannot be obtained, the arc becomes unstable, and the amount of spatter generation increases. On the other hand, if the sum of the Na compound and K compound converted values of Na 2 O and K 2 O exceeds 0.15%, the amount of slag generated in multi-layer welding increases and slag entrainment defects tend to occur. Also, the amount of fumes generated increases. Therefore, the sum of the Na compound and K compound in the flux should be 0.02 to 0.15% in terms of Na 2 O and K 2 O. The Na compound and K compound can be added from the flux, the solid content of water glass composed of sodium silicate and potassium silicate, and the powder of potassium feldspar, sodium fluoride, potassium silicofluoride, and the like.
［鋼製外皮とフラックスの合計でＮｉ、Ｃｒ及びＭｏの１種または２種以上の合計を下記式で０．１５～０．６０］
Ｎｉ、Ｃｒ及びＭｏは、溶接金属の靭性を低下することなく強度を向上する。Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計が下記式で０．１５未満であると、溶接金属の強度向上の効果が得られない。一方、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計が下記式で０．６０を超えると、溶接金属の強度が高くなりすぎて靭性が低下する。したがって、鋼製外皮とフラックスの合計でＮｉ、Ｃｒ及びＭｏの１種または２種以上の合計は下記式で０．１５～０．６０とする。なお、Ｎｉ、Ｃｒ及びＭｏは、鋼製外皮に含まれる成分の他、金属Ｎｉ、金属Ｃｒ、金属Ｍｏ、Ｆｅ－Ｎｉ、Ｆｅ－Ｃｒ、Ｆｅ－Ｍｏ等の合金粉から添加できる。
［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］・・・・式
但し、［ ］は、各成分のワイヤ全質量に対する質量％を示す。
[The sum of one or more of Ni, Cr and Mo in the total of steel skin and flux is 0.15 to 0.60 according to the following formula]
Ni, Cr and Mo improve the strength of the weld metal without reducing its toughness. If the sum of one or more of Ni, Cr and Mo is less than 0.15 in the following formula, the effect of improving the strength of the weld metal cannot be obtained. On the other hand, when the sum of one or more of Ni, Cr and Mo exceeds 0.60 in the following formula, the strength of the weld metal becomes too high and the toughness decreases. Therefore, the total sum of one or more of Ni, Cr and Mo in the steel outer sheath and flux is 0.15 to 0.60 in the following formula. Ni, Cr, and Mo can be added from alloy powders such as metal Ni, metal Cr, metal Mo, Fe--Ni, Fe--Cr, and Fe--Mo, in addition to components contained in the steel outer shell.
[Ni]/3+[Cr]+[Mo] Expression where [ ] indicates mass % of each component with respect to the total mass of the wire.
［鋼製外皮とフラックスの合計でＢ：０．００１５～０．０１５０％］
Ｂは、溶接金属の靭性を向上する。Ｂが０．００１５０％未満であると、溶接金属の靭性向上効果が得られない。一方、Ｂが０．０１５％を超えると、溶接金属に割れが生じやすくなる。したがって、鋼製外皮とフラックスの合計でＢは０．００１５～０．０１５０％とする。なお、Ｂは、鋼製外皮に含まれる成分の他、Ｆｅ－Ｓｉ－Ｂ、Ｆｅ－Ｍｎ－Ｂ等の合金粉から添加できる。
[Total B of steel skin and flux: 0.0015 to 0.0150%]
B improves the toughness of the weld metal. If B is less than 0.00150%, the effect of improving the toughness of the weld metal cannot be obtained. On the other hand, when B exceeds 0.015%, the weld metal tends to crack. Therefore, B is set to 0.0015 to 0.0150% in total of the steel skin and the flux. B can be added from alloy powders such as Fe--Si--B and Fe--Mn--B in addition to components contained in the steel outer shell.
［形成した鋼製外皮の合わせ目を溶接することで鋼製外皮に継目を無くす］
本発明の高電流密度ガスシールドアーク溶接方法に用いるガスシールドアーク溶接用フラックス入りワイヤは、鋼製外皮をパイプ状に成型し、その内部にフラックスを充填した構造である。ワイヤの種類としては、成型した鋼製外皮の合わせ目を溶接して得られる鋼製外皮に継目の無いワイヤと、鋼製外皮の合わせ目の溶接を行わないままとした鋼製外皮に継目を有するワイヤとに大別できる。本発明においては、何れの断面構造のワイヤを採用することができるが、鋼製外皮に合わせ目が無いワイヤは、ワイヤの矯正が容易であることから溶接部へのターゲット性が良好となる。また、鋼製外皮に銅めっきを施すことができるので高速度でワイヤが送給されてもチップの磨耗が少なくなるので、より好ましい。一方、鋼製外皮に合わせ目を有するワイヤは、ワイヤの矯正器でワイヤが周方向に回転しやすく矯正ができず溶接部へのターゲット性が悪くビードが蛇行し易くなる。また、ワイヤ表面に銅めっきを施すことができないので、高速度で長時間ワイヤが送給された場合にはチップ磨耗が大きくアークが不安定となってスパッタ発生量が多くなる。
[Elimination of seams in the steel skin by welding the seams of the formed steel skin]
The flux-cored wire for gas-shielded arc welding used in the high-current-density gas-shielded arc welding method of the present invention has a structure in which a steel outer sheath is formed into a pipe shape, and the interior of the pipe is filled with flux. As for the types of wire, there are two types of wire: a wire without a seam in the steel skin obtained by welding the seam of the molded steel skin, and a steel skin with a seam in which the seam of the steel skin is left unwelded. It can be broadly divided into wires with In the present invention, a wire having any cross-sectional structure can be employed. However, a wire having a seamless steel outer sheath is easy to straighten, and therefore has good targetability to the welded portion. In addition, since the steel sheath can be plated with copper, the wear of the tip is reduced even if the wire is fed at high speed, which is more preferable. On the other hand, a wire having seams in the steel outer sheath tends to rotate in the circumferential direction with a wire straightener and cannot be straightened, resulting in poor targetability to the weld zone and a tendency for the bead to meander. In addition, since the wire surface cannot be plated with copper, when the wire is fed at a high speed for a long time, the tip wears greatly and the arc becomes unstable, resulting in a large amount of spatter.
本発明の高電流密度ガスシールドアーク溶接方法に用いるガスシールドアーク溶接用フラックス入りワイヤの残部は、鋼製外皮のＦｅ、成分調整にために添加する鉄粉のＦｅ分、Ｆｅ－Ｓｉ、Ｆｅ－Ｍｎ、Ｆｅ－Ｔｉ合金等の鉄合金粉のＦｅ分及び不可避不純物である。 The remainder of the flux-cored wire for gas-shielded arc welding used in the high-current-density gas-shielded arc welding method of the present invention includes Fe in the steel outer shell, Fe in iron powder added for component adjustment, Fe—Si, Fe— It is the Fe content and unavoidable impurities in iron alloy powders such as Mn and Fe—Ti alloys.
また、ガスシールドアーク溶接用フラックス入りワイヤのフラックス充填率は特に限定しないが、生産性の観点からワイヤ全質量に対して８～２０％とするのが好ましい。 Although the flux filling rate of the flux-cored wire for gas-shielded arc welding is not particularly limited, it is preferably 8 to 20% with respect to the total mass of the wire from the viewpoint of productivity.
なお、シールドガスは、スパッタ発生量を低減することからＡｒとＣＯ2との混合ガスとするが、ＣＯ2の混合量は５～２５体積％とする。また、シールドガスの流量は高電流密度溶接での耐欠陥性及び大気からの窒素の混入を防ぐために２５～４０リットル／分であることが好ましい。 The shield gas is a mixed gas of Ar and CO 2 in order to reduce the amount of spatter generated, and the mixed amount of CO 2 is 5 to 25% by volume. Also, the flow rate of the shielding gas is preferably 25 to 40 liters/minute in order to prevent defect resistance in high current density welding and to prevent nitrogen from entering from the atmosphere.
以下、実施例により本発明の効果をさらに詳細に説明する。 EXAMPLES Hereinafter, the effects of the present invention will be described in more detail with reference to examples.
まず、鋼製外皮にＪＩＳ Ｇ３１４１ ＳＰＣＣ帯鋼を使用し、表１に示すワイヤ径１．２～１．６ｍｍの鋼製外皮に合わせ目の無いガスシールドアーク溶接用フラックス入りワイヤと鋼製外皮に合わせ目のあるガスシールドアーク溶接用フラックス入りワイヤを試作した。なお、フラックス充填率は１０～１６％とした。 First, JIS G3141 SPCC strip steel is used for the steel sheath, and a seamless flux-cored wire for gas shielded arc welding and steel sheath with a wire diameter of 1.2 to 1.6 mm shown in Table 1 are used. A flux-cored wire for gas-shielded arc welding with seams was experimentally manufactured. Note that the flux filling rate was set to 10 to 16%.
表１に示すガスシールドアーク溶接用フラックス入りワイヤを用いて、板厚２５ｍｍの鋼板（ＪＩＳ Ｇ３１０６ ＳＭ４９０Ａ）を６０°のＶ溝開先（開先深さ１８ｍｍ）に加工し、表２及び表３に示す溶接条件で３層盛溶接をした。 Using the flux-cored wire for gas shielded arc welding shown in Table 1, a steel plate (JIS G3106 SM490A) with a thickness of 25 mm was processed into a 60 ° V groove groove (groove depth 18 mm). Three-layer welding was performed under the welding conditions shown in .
調査項目は、アークの安定性、ビード外観・形状及び３層盛溶接後のスラグ剥離性を調査し、ＪＩＳ ＪＩＳ Ｚ ３１０４に準じてＸ線透過試験を実施して溶接欠陥の有無を調査した後、溶接金属の板表面下７ｍｍから丸棒引張試験片（ＺＩＳ Ｚ３１１１に準じたＡ２号）及び衝撃試験片（Ｖノッチ試験片）を採取して、機械試験を実施した。 The items to be investigated are arc stability, bead appearance/shape, and slag exfoliation after three-layer welding. , A round bar tensile test piece (A2 according to ZIS Z3111) and an impact test piece (V notch test piece) were taken from 7 mm below the plate surface of the weld metal, and a mechanical test was performed.
引張強さの評価は４９０～６２０ＭＰａ、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上を含む場合は５９０～７２０ＭＰａを良好とした。また、靭性の評価は、－２０℃におけるシャルピー衝撃試験を実施し、吸収エネルギーの３回の平均値が６０Ｊ以上、Ｂを含む場合は－３０℃で吸収エネルギーの平均値が６０Ｊ以上を良好とした。 Tensile strength was evaluated at 490 to 620 MPa, and when one or more of Ni, Cr and Mo was included, 590 to 720 MPa was considered good. In addition, for the evaluation of toughness, a Charpy impact test was performed at -20°C, and the average value of absorbed energy for three times was 60J or more, and when B was included, the average value of absorbed energy at -30°C was 60J or more. bottom.
スパッタ発生量は、銅製の捕集箱を用いて、板厚１２ｍｍの鋼板（ＪＩＳ Ｇ３１０６ ＳＭ４９０Ａ）に表２に示す溶接条件で３０秒間の繰り返し５回溶接を行い、１分間当りのスパッタ発生量を算出した。１分間当りスパッタ発生量が１．０ｇ以下を良好と評価した。それらの結果を表３にまとめて示す。 The amount of spatter generated was measured by welding a steel plate (JIS G3106 SM490A) with a thickness of 12 mm (JIS G3106 SM490A) with a thickness of 12 mm five times for 30 seconds under the welding conditions shown in Table 2 using a copper collection box, and measuring the amount of spatter generated per minute. Calculated. A spatter generation amount of 1.0 g or less per minute was evaluated as good. These results are summarized in Table 3.
表３中試験Ｎｏ．１～Ｎｏ．１５が本発明例、試験Ｎｏ．１６～Ｎｏ．３０は比較例である。本発明例である試験Ｎｏ．１～Ｎｏ．１５は、高電流密度の溶接条件、組み合わせたワイヤ記号Ｗ１～Ｗ１５のＣ、Ｓｉ、Ｍｎ、Ｓ、Ｃｕ、Ｔｉ、Ａｌ、弗素化合物のＦ換算値の合計、ＳｉＯ2、Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計量が適正であるので、アークが安定しスパッタ発生量が少なく、ビード外観・形状及びスラグ剥離性が良好であり溶接欠陥が無く、溶接金属の引張強さ及び吸収エネルギーが良好であるなど極めて満足な結果であった。なお、試験Ｎｏ．５～１２は、組み合わせたワイヤ記号Ｗ５～Ｗ１２のＮｉ、Ｃｒ及びＭｏの１種または２種以上の合計が［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］で適量含むので溶接金属の吸収エネルギーを低下させること無く高い引張強さが得られた。また、試験Ｎｏ．９～１５は、組み合わせたワイヤ記号Ｗ９～Ｗ１５にＢを適量含むので－３０℃における吸収エネルギーが良好であった。試験Ｎｏ．３、Ｎｏ．６及び試験Ｎｏ．１１は、組み合わせたワイヤ記号Ｗ３、Ｗ６及びＷ１１の鋼製外皮に継目を有するのでややビードが蛇行した。 Test No. in Table 3. 1 to No. 15 is an example of the present invention, test No. 16 to No. 30 is a comparative example. Test No., which is an example of the present invention. 1 to No. 15 is the welding condition of high current density, the combined wire symbols W1 to W15 of C, Si, Mn, S, Cu, Ti, Al, the sum of F conversion values of fluorine compounds, SiO 2 , Na compounds and K compounds Since the total amount of Na 2 O conversion value and K 2 O conversion value is appropriate, the arc is stable, the amount of spatter is small, the appearance and shape of the bead and the slag peelability are good, there are no welding defects, and the weld metal is excellent. The results were extremely satisfactory, such as good tensile strength and good absorbed energy. In addition, test No. 5 to 12 contain an appropriate amount of [Ni]/3 + [Cr] + [Mo] of one or more of Ni, Cr and Mo of the combined wire symbols W5 to W12, so the absorbed energy of the weld metal is reduced. A high tensile strength was obtained without degradation. Also, test no. Nos. 9 to 15 contained an appropriate amount of B in the combined wire symbols W9 to W15, so the absorbed energy at -30°C was good. Test no. 3, No. 6 and test no. 11 had a seam in the steel skin of the combined wire symbols W3, W6 and W11, resulting in a slightly meandering bead.
比較例中試験Ｎｏ．１６は、電流密度が低いので、溶接金属の溶着量が少なかった。 Comparative Example Test No. In No. 16, since the current density was low, the deposition amount of the weld metal was small.
試験Ｎｏ．１７は、電流密度が高いので、スパッタ発生量が多かった。また、組み合わせたワイヤ記号Ｗ１１の鋼製外皮に継目を有するのでややビードが蛇行した。 Test no. In No. 17, the amount of spatter generated was large due to the high current density. In addition, since the steel sheath of the combined wire symbol W11 has a seam, the bead slightly meanders.
試験Ｎｏ．１８は、組み合わせたワイヤ記号Ｗ１６のＣが少ないので、溶接金属の引張強さが低かった。また、ＳｉＯ2が多いので、スラグ巻き込み欠陥が生じ、溶接金属の吸収エネルギーが低値であった。 Test no. No. 18 had less C in the combined wire symbol W16, so the tensile strength of the weld metal was low. In addition, since the SiO 2 content was large, slag entrainment defects occurred, and the absorbed energy of the weld metal was low.
試験Ｎｏ．１９は、電流密度が低いので、溶接金属の溶着量が少なかった。また、組み合わせたワイヤ記号Ｗ１７のＣが多いので、スパッタ発生量が多く、溶接金属の引張強さが高く吸収エネルギーが低かった。さらに、Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計量が多いので、ヒューム発生量が多くスラグ巻き込みも生じた。 Test no. In No. 19, since the current density was low, the deposition amount of the weld metal was small. In addition, since there was a large amount of C in the combined wire symbol W17, a large amount of spatter was generated, the tensile strength of the weld metal was high, and the absorbed energy was low. Furthermore, since the total amount of Na compound and K compound converted to Na 2 O and converted to K 2 O was large, a large amount of fumes was generated and slag entrainment occurred.
試験Ｎｏ．２０は、組み合わせたワイヤ記号Ｗ１８のＳｉが少ないので、溶接金属の引張強さが低く吸収エネルギーも低値であった。また、ＳｉＯ2が少ないので、ビード止端部のなじみが悪くビード外観・形状が不良であった。 Test no. In No. 20, the combined wire symbol W18 contained less Si, so the tensile strength of the weld metal was low and the absorbed energy was also low. Moreover, since the amount of SiO 2 was small, the conformability of the toe of the bead was poor, and the appearance and shape of the bead were poor.
試験Ｎｏ．２１は、組み合わせたワイヤ記号Ｗ１９のＳｉが多いので、溶接金属の引張強さが高く吸収エネルギーが低かった。また、Ｓが多いので、クレータ割れが生じた。さらに、鋼製外皮に継目を有するのでややビードが蛇行した。 Test no. In No. 21, the combined wire symbol W19 contained a large amount of Si, so the tensile strength of the weld metal was high and the absorbed energy was low. In addition, since the amount of S was large, crater cracks occurred. Furthermore, since the steel outer skin has a seam, the bead is slightly meandering.
試験Ｎｏ．２２は、電流密度が高いので、スパッタ発生量が多かった。また、組み合わせたワイヤ記号Ｗ２０のＭｎが少ないので、溶接金属の引張強さが低く吸収エネルギーも低値であった。さらに、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計が［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］で少ないので、溶接金属の引張強さ向上の効果が得られなかった。 Test no. In No. 22, a large amount of spatter was generated due to the high current density. In addition, since the combined wire symbol W20 has a small amount of Mn, the tensile strength of the weld metal is low and the absorbed energy is also low. Furthermore, since the sum of one or more of Ni, Cr and Mo is small at [Ni]/3+[Cr]+[Mo], the effect of improving the tensile strength of the weld metal was not obtained.
試験Ｎｏ．２３は、組み合わせたワイヤ記号Ｗ２１のＭｎが多いので、溶接金属の引張強さが高く吸収エネルギーが低かった。また、Ｂが少ないので、吸収エネルギーの向上効果は得られなかった。 Test no. In No. 23, the combined wire symbol W21 had a large amount of Mn, so the tensile strength of the weld metal was high and the absorbed energy was low. Also, since the amount of B was small, the effect of improving the absorbed energy was not obtained.
試験Ｎｏ．２４は、組み合わせたワイヤ記号Ｗ２２のＳが少ないので、スラグ剥離性が不良であった。また、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計が［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］で多いので、溶接金属の引張強さが高くなりすぎて吸収エネルギーが低かった。 Test no. In No. 24, the combined wire symbol W22 had a small amount of S, so the slag removability was poor. In addition, since the sum of one or more of Ni, Cr and Mo was large at [Ni]/3+[Cr]+[Mo], the tensile strength of the weld metal was too high and the absorbed energy was low.
試験Ｎｏ．２５は、組み合わせたワイヤ記号Ｗ２３のＢが多いので、クレータ割れが生じた。また、Ａｌが多いので、アークが不安定でスパッタ発生量が多かった。 Test no. In No. 25, crater cracks occurred because there were many Bs of the combined wire symbol W23. In addition, since the amount of Al was large, the arc was unstable and a large amount of spatter was generated.
試験Ｎｏ．２６は、組み合わせたワイヤ記号Ｗ２４のＣｕが少ないので、溶接金属の吸収エネルギーが低値であった。また、Ｂが少ないので、吸収エネルギー向上の効果が得られなかった。 Test no. In No. 26, the absorbed energy of the weld metal was low because the combined wire symbol W24 contained less Cu. In addition, since the amount of B was small, the effect of improving the absorbed energy was not obtained.
試験Ｎｏ．２７は、組み合わせたワイヤ記号Ｗ２５のＣｕが多いので、溶接金属の吸収エネルギーが低値であった。また、Ｎａ化合物及びＫ化合物のＮａ2Ｏ換算値とＫ2Ｏ換算値の合計量が少ないので、アークが不安定でスパッタ発生量が多かった。さらに、Ｎｉ、Ｃｒ及びＭｏの１種または２種以上の合計が［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］で少ないので、溶接金属の引張強さ向上の効果が得られなかった。 Test no. No. 27 has a large amount of Cu in the combined wire symbol W25, so the absorbed energy of the weld metal was low. In addition, since the total amount of Na compound and K compound converted to Na 2 O and converted to K 2 O was small, the arc was unstable and a large amount of spatter was generated. Furthermore, since the sum of one or more of Ni, Cr and Mo is small at [Ni]/3+[Cr]+[Mo], the effect of improving the tensile strength of the weld metal was not obtained.
試験Ｎｏ．２８は、組み合わせたワイヤ記号Ｗ２６のＴｉ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、溶接金属の吸収エネルギーが低値であった。さらに、鋼製外皮に継目を有するのでややビードが蛇行した。 Test no. In No. 28, the amount of Ti in the combined wire symbol W26 was small, so the arc was unstable and the amount of spatter generated was large. Also, the absorbed energy of the weld metal was low. Furthermore, since the steel outer skin has a seam, the bead is slightly meandering.
試験Ｎｏ．２９は、組み合わせたワイヤ記号Ｗ２７のＴｉが多いので、溶接金属の吸収エネルギーが低値であった。また、弗素化合物のＦ換算値が多いので、アークが荒くなりスパッタ発生量が多かった。 Test no. No. 29 had a large amount of Ti in the combined wire symbol W27, so the absorbed energy of the weld metal was low. In addition, since the F conversion value of the fluorine compound was large, the arc was rough and the amount of spatter generated was large.
試験Ｎｏ．３０は、組み合わせたワイヤ記号Ｗ２８のＡｌが少ないので、溶接金属の引張強さが低く吸収エネルギーも低値であった。また、弗素化合物のＦ換算値が少ないので、アークが集中せずスパッタ発生量が多かった。 Test no. In No. 30, the combined wire symbol W28 contained less Al, so the tensile strength of the weld metal was low and the absorbed energy was also low. In addition, since the F conversion value of the fluorine compound was small, the arc was not concentrated and a large amount of spatter was generated.
Claims (4)
ワイヤ全質量に対する質量％で、鋼製外皮とフラックスの合計で、
Ｃ：０．０３～０．１２％、
Ｓｉ：０．２～１．０％、
Ｍｎ：１．０～２．５％、
Ｓ：０．０１～０．０３％、
Ｃｕ：０．０５～０．４５％、
Ｔｉ：０．０８～０．２０％、
Ａｌ：０．０３～０．１５％を含有し、
さらに、ワイヤ全質量に対する質量％で、フラックス中に、
弗素化合物：Ｆ換算値の合計で０．０１～０．１０％、
ＳｉＯ2：０．０１～０．２０％、
Ｎａ化合物及びＫ化合物：Ｎａ2Ｏ換算値とＫ2Ｏ換算値の合計で０．０２～０．１５％を含有し、残部は鋼製外皮のＦｅ、鉄粉のＦｅ分、鉄合金粉のＦｅ分及び不可避不純物からなるガスシールドアーク溶接用フラックス入りワイヤを用い、電流密度が３２０～５２０Ａ／ｍｍ2の条件で溶接することを特徴する高電流密度ガスシールドアーク溶接方法。 In a high-current density gas-shielded arc welding method in which welding is performed using a flux-cored wire for gas-shielded arc welding in which a steel outer sheath is filled with flux as an electrode,
% by mass of the total mass of the wire, the sum of the steel sheath and flux,
C: 0.03 to 0.12%,
Si: 0.2 to 1.0%,
Mn: 1.0-2.5%,
S: 0.01 to 0.03%,
Cu: 0.05-0.45%,
Ti: 0.08 to 0.20%,
Al: contains 0.03 to 0.15%,
In addition, in mass % with respect to the total mass of the wire, in the flux,
Fluorine compound: 0.01 to 0.10% in total F conversion value,
SiO 2 : 0.01 to 0.20%,
Na compound and K compound: 0.02 to 0.15% in total of Na 2 O conversion value and K 2 O conversion value, the balance being Fe in the steel outer shell, Fe content in the iron powder, and Fe content in the iron alloy powder A high-current-density gas-shielded arc welding method characterized by using a flux-cored wire for gas-shielded arc welding containing Fe and unavoidable impurities and welding under conditions of a current density of 320 to 520 A/mm 2 .
［Ｎｉ］／３＋［Ｃｒ］＋［Ｍｏ］・・・・式
但し、［ ］は、各成分のワイヤ全質量に対する質量％を示す。 Welding is performed with the flux-cored wire for gas-shielded arc welding, which further contains 0.15 to 0.60 of Ni, Cr, and Mo in total of one or more of Ni, Cr, and Mo in the sum of the steel skin and flux, according to the following formula. The high-current density gas-shielded arc welding method according to claim 1, characterized in that:
[Ni]/3+[Cr]+[Mo] Expression where [ ] indicates mass % of each component with respect to the total mass of the wire.
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