Gas shielded arc welding wire

Abstract

To provide welded part limited in sputtering during welding, capable of making steps as elimination of slugs unnecessary after the welding and exhibiting excellent electro deposition, and having a good bead shape.SOLUTION: A wire for gas shield arc-welding contains, by mass% with respect to a wire total mass: Mn of 1.88-2.70%; Ti of 0.10-0.40%; O of over 0.0050 to 0.0105% or lower; C of 0.01-0.10%; Si of 0.05-0.50%; Cu of 0.01-0.30%; 0.001-0.020%; Al of 0.10 or lower; and P of 0.025% or lower, and the remainder is Fe and inevitable impurities. When contents of Ti and O are respectively represented as [Ti] and [O] by mass%, values calculated by an expression (1): 1000×[Ti]×[O] / ([Ti]+50×[O]) are 2.13-4.30.SELECTED DRAWING: None

Description

[Technical Field]

[0001] The present invention relates to a wire for gas-shielded arc welding. [Background technology]

[0002] In recent years, due to the increasing demand for environmental performance, technological development to improve the fuel efficiency of automobiles and other vehicles has been actively promoted. Methods for improving the fuel efficiency of automobiles and other vehicles include improving the efficiency of internal combustion engines, hybridization, and electrification. As electrification tends to increase the weight of the vehicle body due to the installation of batteries, development of weight-reducing technologies is also being promoted at the same time. For example, attempts are being actively made to reduce the weight of vehicles by using thin steel plates with higher strength than conventional steel plates, thereby reducing the plate thickness.

[0003] Because suspension parts are exposed to a corrosive environment due to moisture from the road surface and salt damage contained in snow-melting agents, localized thinning of steel plates is an issue. Therefore, in order to further reduce the weight of vehicles, suspension parts that have sufficient strength and durability even when made thinner are required, and technology that can prevent corrosion of suspension parts is also needed.

[0004] A common method for protecting undercarriage components from corrosive environments is to apply electrodeposition coating after arc welding. However, when electrodeposition coating is performed after welding, the electrodeposition coating film does not form on the welding slag, resulting in coating defects, which can cause corrosion to progress from these defects. Therefore, methods for forming thick electrodeposition coating films have been used to prevent the occurrence of welding defects. However, even if a coating film is formed on the slag, the coating film may peel off along with the slag due to the force applied during driving, which can lead to corrosion progressing from the peeled-off areas.

[0005] Furthermore, among suspension components, those closer to the road surface or thinner components have been treated with galvanized steel sheets to improve corrosion resistance even if the coating peels off, due to the sacrificial corrosion protection effect of zinc. However, in welds, the zinc vaporizes due to the heat generated during arc welding, so the effect of improving corrosion resistance at the weld bead cannot be fully expected. As a result, there is a risk of corrosion occurring due to poor coating on the welding slag, or even if a coating is formed, corrosion may occur due to slag peeling during driving.

[0006] For example, Patent Document 1 proposes a welding wire in which the contents of C, Si, and Mn are adjusted, and the total content of one or more elements selected from Zr, Ti, and Al is adjusted, in order to prevent a coating film from being formed on the slag-covered portion when electrodeposition coating is performed after welding, thereby reducing the durability of the part. Patent Document 1 discloses that the wire has good removability of slag adhering to the weld after welding, making it possible to remove the slag significantly easily. In recent years, methods of physically removing slag after welding have been used, particularly in luxury cars, to ensure reliability.

[0007] Patent Document 2 discloses a gas-shielded arc welding wire in which the contents of C, Si, Mn, Ti, Cu, S, N, Al, and P in the wire are controlled and the ratio of the Ti content to the Si content is appropriately specified. Patent Document 2 also describes that the O content in the wire is preferably 0.0050 mass% or less. [Prior art documents] [Patent documents]

[0008] [Patent Document 1] Japanese Patent Publication No. 62-124095 [Patent Document 2] Patent No. 6771638 Summary of the Invention [Problem to be solved by the invention]

[0009] However, when the wire described in Patent Document 1 is used, the addition of a slag removal step increases the number of manufacturing steps and increases manufacturing costs. Also, in consideration of workability during arc welding, a wire that generates less spatter is required. Furthermore, welded joints such as lap fillets are prone to stress concentration due to their discontinuous shape, which, when combined with corrosion thinning, can lead to fatigue fractures. Therefore, the bead toe must be smooth and have few weld defects.

[0010] On the other hand, the wire described in Patent Document 2 generates less spatter during welding, has excellent electrodeposition coatability, and can produce welds with a good bead shape. However, in recent years, there has been a demand for further improvements in electrodeposition coatability and welding workability. In addition, there is a need for the development of a wire that can fully achieve the above effects even when the O content deviates from the range described in Patent Document 2.

[0011] The present invention has been made in view of the above-mentioned circumstances, and has an object to provide a gas-shielded arc welding wire that generates little spatter during welding, does not require a step such as slag removal after welding, has excellent electrodeposition coatability, and can obtain a weld with a good bead shape. [Means for solving the problem]

[0012] As a result of extensive research aimed at solving the above problems, the inventors discovered that by uniformly forming a thin slag at the weld, excellent electrodeposition coatability can be achieved without the need for slag removal after welding. Specifically, by appropriately adjusting the relationship between the Ti and O contents in the wire and appropriately controlling the balance of each component, it is possible to uniformly form a thin slag at the weld that produces little spatter during welding, has a good bead shape, and has high adhesion. Furthermore, the presence of the thin slag makes it possible to prevent defects from occurring in the coating film formed by electrodeposition coating on the weld. Although the mechanism by which the uniform formation of a thin slag after welding results in the uniform formation of an electrodeposition coating film across the entire surface is unclear, it is speculated that this may be due to the difference in conductivity between thin and thick slag. Furthermore, when a thick electrodeposition coating film is formed, the coating film peels off along with the slag. It is speculated that the reason this occurs is because the coating film is formed on top of the uneven, peelable slag, creating steps on the surface of the part, making it more susceptible to force being applied during running. The present invention was made based on these findings.

[0013] The above object of the present invention is achieved by the following configuration [1] relating to a gas-shielded arc welding wire.

[0014] [1] Per total wire mass, Mn: 1.88 mass% or more and 2.70 mass% or less, Ti: 0.10% by mass or more and 0.40% by mass or less, O: more than 0.0050 mass% and 0.0105 mass% or less, C: 0.01% by mass or more and 0.10% by mass or less, Si: 0.05% by mass or more and 0.50% by mass or less, Cu: 0.01% by mass or more and 0.30% by mass or less, S: 0.001% by mass or more and 0.020% by mass or less, Contains Al: 0.10% by mass or less, P: 0.025% by mass or less, The balance is Fe and unavoidable impurities, When the Ti content per total mass of the wire is expressed as [Ti] in mass% and the O content per total mass of the wire is expressed as [O] in mass%, A gas-shielded arc welding wire characterized in that the value calculated by the formula (1): 1000 × [Ti] × [O] / ([Ti] + 50 × [O]) is 2.13 or more and 4.30 or less.

[0015] Furthermore, preferred embodiments of the present invention relating to a gas-shielded arc welding wire relate to the following [2] and [3].

[0016] [2] The wire for gas-shielded arc welding according to [1], characterized in that the Si content is 0.25 mass % or less.

[0017] [3] The wire for gas-shielded arc welding according to [1] or [2], characterized in that the Ti content is 0.15 mass % or more. [Effects of the Invention]

[0018] According to the present invention, it is possible to provide a gas-shielded arc welding wire that generates little spatter during welding, does not require steps such as slag removal after welding, has excellent electrodeposition paintability, and can produce welds with a good bead shape. [Brief explanation of the drawings]

[0019] [Figure 1] FIG. 1 is a perspective view showing gas-shielded arc welding conditions. [Figure 2] FIG. 2 is a side view showing the gas shielded arc welding conditions. DETAILED DESCRIPTION OF THE INVENTION

[0020] Hereinafter, embodiments for implementing the present invention will be described in detail. Note that the present invention is not limited to the embodiments described below, and can be arbitrarily modified and implemented without departing from the gist of the present invention. Hereinafter, the components contained in the wire for gas shielded arc welding according to the present embodiment will be described in detail regarding the reasons for addition and the reasons for numerical limitation. In the following description, the amount of each component in the wire is defined as the content relative to the total mass of the wire.

[0021] <Mn: 1.88 mass% or more and 2.70 mass% or less> Mn is an important component for ensuring the desired strength of the weld metal. Also, since MnO has higher conductivity compared to SiO2, forming a composite slag containing more Mn makes it easier for a coating film to be uniformly formed on the slag in electrodeposition coating after welding. When the Mn content in the wire is 1.88 mass% or more, the strength of the weld metal can be sufficiently obtained, and the effect of forming a coating film on the slag can be sufficiently obtained. Therefore, the Mn content in the wire is set to 1.88 mass% or more per total mass of the wire, preferably 1.95 mass% or more, more preferably 2.00 mass% or more, and still more preferably 2.10 mass% or more. On the other hand, when the Mn content in the wire exceeds 2.70 mass%, excessive deoxidation progresses and the amount of oxygen in the molten pool decreases. As a result, the viscosity and surface tension of the molten droplet increase, damaging the bead shape. Therefore, the Mn content in the wire is set to 2.70 mass% or less per total mass of the wire, preferably 2.60 mass% or less, more preferably 2.50 mass% or less, and still more preferably 2.40 mass% or less.

[0022] <Ti: 0.10 mass% or more and 0.40 mass% or less> Ti is one of the important elements in the wire according to the present embodiment. When titanium oxide is dispersed in the slag, the formation of Si-based slag is inhibited. As a result, the electrodeposition coating property can be improved, and excellent rust prevention property can be obtained. When the Ti content in the wire is 0.10% by mass or more, the effect of improving the electrodeposition coating property by inhibiting the formation of Si-based slag can be sufficiently obtained. Therefore, the Ti content in the wire is 0.10% by mass or more per total mass of the wire, preferably 0.15% by mass or more, more preferably 0.21% by mass or more, and still more preferably more than 0.25% by mass. On the other hand, when the Ti content in the wire exceeds 0.40% by mass, excessive deoxidation progresses, the amount of slag formation increases too much, the slag thickens, and the bead shape deteriorates due to excessive progress of the deoxidation action. Therefore, the Ti content in the wire is 0.40% by mass or less per total mass of the wire, preferably 0.35% by mass or less, and more preferably 0.30% by mass or less.

[0023] <O: More than 0.0050% by mass and 0.0105% by mass or less> O is an element that can reduce viscosity and surface tension and improve the detachment of droplets during welding. When the O content in the wire exceeds 0.0050% by mass, the detachment of droplets improves, and the generation of large-droplet spatter during short circuit can be reduced. Therefore, the O content in the wire is more than 0.0050% by mass per total mass of the wire, preferably 0.0060% by mass or more, more preferably 0.0065% by mass or more, and still more preferably 0.0070% by mass or more. On the other hand, when the O content in the wire exceeds 0.0105% by mass, the droplet transfer at the tip of the wire during arc welding is likely to be disturbed, the molten pool vibrates greatly along with short circuit, and the end shape deteriorates, resulting in a poor bead shape. Therefore, the O content in the wire is 0.0105% by mass or less per total mass of the wire, preferably 0.0100% by mass or less, more preferably 0.0090% by mass or less, and still more preferably 0.0085% by mass or less.

[0024] <C: 0.01% by mass or more and 0.10% by mass or less> C is a component that has a deoxidizing effect and also has the effect of increasing the strength of the weld metal. In the welding of thin plates, since single-pass welding is applied, there is no risk of strength reduction due to reheat as in the case of multi-layer welding, and it is possible to obtain a strength equal to or higher than that of the base metal. When the C content in the wire is less than 0.01% by mass, it becomes difficult to obtain the minimum required strength of mild steel. Therefore, the C content in the wire shall be 0.01% by mass or more, preferably 0.02% by mass or more, and more preferably 0.03% by mass or more per total mass of the wire. On the other hand, when the C content in the wire exceeds 0.10% by mass, the deoxidizing effect becomes large and the viscosity of the droplet increases, so it is easy to short-circuit and spatter is likely to occur. Also, by combining with oxygen, CO is generated near the arc, and spatter due to explosion is likely to occur, and the amount of fume increases. Therefore, within the range where the desired strength of the weld metal can be ensured, it is preferable that the C content is less. Thus, the C content in the wire shall be 0.10% by mass or less, preferably less than 0.09% by mass, and more preferably less than 0.08% by mass per total mass of the wire.

[0025] <Si: 0.05% by mass or more and 0.50% by mass or less> Si is a component that has a deoxidizing effect and also has the effect of improving the bead appearance of the weld. When the Si content in the wire is 0.05% by mass or more, the shape of the weld termination part can be made into a smooth bead shape. Also, the Si phase present in the slag can enhance the adhesion between the slag and the weld metal, and thereby the rust prevention property can also be improved. Furthermore, when an appropriate amount of Si is contained, spatter during welding is reduced. Therefore, the Si content in the wire shall be 0.05% by mass or more, preferably 0.10% by mass or more, more preferably 0.12% by mass or more, and even more preferably 0.15% by mass or more per total mass of the wire in order to further suppress the generation of spatter. On the one hand, when the Si content in the wire exceeds 0.50% by mass, the slag formed by the combination of Si and oxygen in the wire tends to agglomerate, and the thickness of the slag increases. As a result, it becomes difficult to form an electrodeposition coating film on the surface of the slag, and coating defects occur. Therefore, the Si content in the wire is 0.50% by mass or less per total mass of the wire, preferably 0.40% by mass or less, more preferably 0.35% by mass or less, still more preferably 0.30% by mass or less, and particularly preferably 0.25% by mass or less.

[0026] <Cu: 0.01% by mass or more and 0.30% by mass or less> Cu is a component having the effect of improving the rust resistance of the wire. When the Cu content in the wire is 0.01% by mass or more, the effect of improving the rust resistance of the wire can be sufficiently obtained. Therefore, the Cu content in the wire is 0.01% by mass or more per total mass of the wire, preferably 0.05% by mass or more, more preferably 0.10% by mass or more, and still more preferably 0.15% by mass or more. On the other hand, when the Cu content in the wire exceeds 0.30% by mass, the required crack resistance cannot be obtained. Therefore, the Cu content in the wire is 0.30% by mass or less per total mass of the wire, preferably 0.25% by mass or less, and more preferably 0.20% by mass or less.

[0027] <S: 0.001% by mass or more and 0.020% by mass or less> S has the effect of aggregating slag and is an element that improves the wettability of the weld bead. For example, when the S content in the wire is changed while keeping the amount of slag constant, as the S content increases, the slag aggregates and the thickness increases. Therefore, for electrodeposition coating properties, the lower the S content, the more preferable. On the other hand, for the wettability of the weld bead, the higher the S content, the more preferable. When the S content in the wire is less than 0.001% by mass, the wettability of the weld bead becomes poor. Therefore, the S content in the wire is 0.001% by mass or more per total mass of the wire, preferably 0.003% by mass or more, and more preferably 0.005% by mass or more. On the one hand, when the S content in the wire exceeds 0.020% by mass, it becomes difficult to uniformly form a thin slag on the weld metal, and there is a risk that the electrodeposition coating film may not be formed or may peel off together with the slag. Therefore, the S content in the wire should be 0.020% by mass or less per total mass of the wire, preferably 0.015% by mass or less, and more preferably 0.010% by mass or less.

[0028] <Al: 0.10% by mass or less (including 0% by mass)> Al is a component that has a deoxidizing effect and an effect of changing the physical properties of the slag. Specifically, since Al has an effect of aggregating the slag, it is an element that reduces the adhesion of the slag. Therefore, the Al content in the wire may be 0% by mass. When the Al content in the wire exceeds 0.10% by mass, the adhesion of the slag decreases and the electrodeposition coating property deteriorates. Therefore, the Al content in the wire should be 0.10% by mass or less per total mass of the wire, preferably 0.05% by mass or less, and more preferably 0.03% by mass or less. When Al is contained, it is preferably 0.001% by mass or more.

[0029] <P: 0.025% by mass or less (including 0% by mass)> P is an element that reduces the crack resistance of the weld metal. The lower the P content in the wire, the more preferable it is, and it may be 0% by mass. When the P content in the wire exceeds 0.025% by mass, the required crack resistance cannot be obtained. Therefore, the P content in the wire should be 0.025% by mass or less per total mass of the wire, preferably 0.020% by mass or less, more preferably 0.015% by mass or less, and even more preferably 0.010% by mass or less.

[0030] <Value calculated by formula (1): 2.13 or more and 4.30 or less> The inventors have found a relational expression represented by the following formula (1) using the Ti content and O content in the wire, and have discovered that the state of slag, the amount of slag, etc. can be controlled by appropriately controlling the value calculated by this formula (1).

[0031] Formula (1): 1000×[Ti]×[O] / ([Ti]+50×[O]) Here, [Ti] is the value of the Ti content per total mass of the wire expressed in mass %, and [O] is the value of the O content per total mass of the wire expressed in mass %.

[0032] By appropriately adjusting the value calculated by the above formula (1), it is possible to control the amount of Ti oxide in the slag and reduce the proportion of Si-based slag. Furthermore, the adhesion of the slag can be improved, resulting in improved electrodeposition coatability. When the value calculated by the above formula (1) is 2.13 or higher, the amount of Ti oxide in the slag increases and the proportion of Si-based slag decreases, resulting in excellent electrodeposition coatability. Therefore, the value calculated by the above formula (1) should be 2.13 or higher, preferably 2.25 or higher, and more preferably 2.40 or higher.

[0033] On the other hand, if the value calculated by the above formula (1) exceeds 4.30, the contents of Ti and O become excessive, causing excessive deoxidation, resulting in the formation of thick slag and deteriorating electrodeposition coatability. Therefore, the value calculated by the above formula (1) should be 4.30 or less, preferably 4.00 or less, and more preferably 3.50 or less.

[0034] <Remainder> The remainder of the wire according to this embodiment is Fe and unavoidable impurities, such as Zr, Ni, Co, Li, Sn, Sb, Bi, B, Cr, Mo, N, and As. The wire according to this embodiment may contain, among the above-mentioned inevitable impurities, for example, Ni, Co, B, Sb, etc., in the ranges of Ni: 0.10 mass% or less, Co: 0.10 mass% or less, B: 0.01 mass% or less, Sb: 0.01 mass% or less, Cr: 0.10 mass% or less, and Mo: 0.10 mass% or less.

[0035] <Shielding gas: Ar-CO2 mixed gas> The wire according to this embodiment can use, for example, an Ar-CO2 mixed gas as a shielding gas. When an Ar-CO2 mixed gas is used, the amount of oxygen contained in the shielding gas is small, so the amount of slag generated by oxidation is reduced. The ratio of the Ar-CO2 mixed gas can be, for example, 80% by volume of Ar and 20% by volume of CO2 mixed gas.

[0036] The welding position using the wire according to the present embodiment is not particularly limited. Furthermore, the wire diameter of the wire according to the present embodiment is not particularly limited, but can be applied to wires having diameters specified in welding material standards such as AWS or JIS.

[0037] <Wire manufacturing> No special manufacturing conditions are required to manufacture the wire according to this embodiment, and it can be manufactured by a conventional method. For example, steel having the above-mentioned components is melted to obtain an ingot. The ingot is subjected to hot forging or the like as needed, followed by hot rolling and cold drawing to form a wire. The wire is annealed at a temperature of about 500 to 900°C as needed, pickled, copper plated, and further subjected to finish drawing as needed to obtain a target wire diameter. Thereafter, a lubricant is added as needed to form a welding wire. [Example]

[0038] The effects of the present invention will be specifically explained below with reference to examples and comparative examples, but the present invention is not limited thereto.

[0039] [Wire manufacturing] Gas shielded arc welding wires with a wire diameter of 1.2 mm were produced so that the chemical components of the wires would have various contents.

[0040] [Gas-shielded arc welding] Figure 1 is a perspective view showing the gas-shielded arc welding conditions using wires of an example of the present invention and a comparative example, and Figure 2 is a side view thereof. Two plate-shaped steel plates 1 and 2, each 150 mm long, 50 mm wide, and 2.9 mm thick, were horizontally arranged in an overlapping state with a 20 mm offset in the width direction (root spacing: 0 mm), and horizontal fillet welding was performed on a fillet portion formed between the top surface of the lower steel plate 1 and the side surface of the upper steel plate 2 using each of the gas-shielded arc welding wires of the example of the present invention and the comparative example under the welding conditions shown in Table 1 below.

[0041] Welding was started at a position 15 mm from one end of the steel plates 1 and 2 in the longitudinal direction, and proceeded for a distance of 120 mm in the direction of arrow A. After that, welding was terminated at a position 15 mm from the other end of the steel plates 1 and 2 in the longitudinal direction, which is opposite to the welding start position, to form weld metal 3. As shown in Fig. 2, the angle of welding torch 4 was 45° with respect to the perpendicular direction of steel plate 1, and the aimed position of wire 4a was a position approximately 0.5 mm away from the end face of steel plate 2 in the width direction.

[0042] Wire Evaluation <Slag adhesion> After welding, the weld metal surface was struck with a chisel, and the slag adhesion was evaluated by checking whether the slag fell off. Regarding slag adhesion, those in which the slag did not fall off the weld metal surface were rated as ○ (good), and those in which the slag easily peeled off and fell off were rated × (poor).

[0043] <Rust prevention> After welding, a coating was formed on the surface of the joined components by electrodeposition coating, and then a cyclic corrosion test was conducted in accordance with JIS K 5600-7-9 to evaluate rust prevention, which serves as an index of electrodeposition paintability. Regarding rust prevention, specimens in which the rust area ratio on the weld bead after 30 cycles of the cyclic corrosion test was 0 to less than 20% were rated as ○ (good), and specimens in which the rust area ratio was 20% or more were rated × (poor). Note that for some test specimens, the cyclic corrosion test was not conducted, and specimens in which a thin layer of slag had spread on the weld metal, resulting in good electrodeposition paintability, were rated as ○ (good), and specimens in which the slag had aggregated on the weld metal, resulting in poor electrodeposition paintability, were rated × (poor).

[0044] <Low spatter> Based on the sensory evaluation during pulse welding, those with little spatter were rated "A" (good), those with slightly less spatter were rated "B" (fair), and those with many short circuits and a lot of spatter were rated "C" (poor).

[0045] <Bead shape> The cross section of the fillet weld was embedded in resin and the weld toe on the lower plate side was observed at 50x magnification, and a particularly smooth shape was rated "A" (excellent), a smooth shape was rated "B" (good), and a poor fit and poor shape was rated "C" (poor).

[0046] The chemical composition of each wire used is shown in Table 2 below, and the evaluation results of each test are shown in Table 3 below. The remainder of the wire's chemical composition is Fe and unavoidable impurities, and the amount of each component in the wire is shown as the content (mass%) relative to the total mass of the wire. In Table 2, formula (1) represents 1000 × [Ti] × [O] / ([Ti] + 50 × [O]). In Table 2, "-" in the Al column means that the content is less than 0.001 mass%. In addition, in the evaluation results column shown in Table 3, "-" means that the evaluation was not performed.

[0047] [Table 1]

[0048] [Table 2]

[0049] [Table 3]

[0050] As shown in Tables 2 and 3 above, inventive examples 1 to 5, the wire components and the values ​​obtained by formula (1) were within the ranges of the present invention, so spatter during welding was small and the bead shape was good. Furthermore, these inventive examples had good slag adhesion, and an electrodeposition coating film could be formed in good condition without removing the slag, thereby achieving excellent rust prevention.

[0051] On the other hand, in Comparative Example No. 1, the O content in the wire exceeded the upper limit of the range defined in the present invention, and therefore the bead shape was poor.

[0052] In Comparative Example No. 2, the Si content in the wire exceeded the upper limit of the range specified in the present invention, and therefore the slag adhesion was reduced, resulting in poor rust prevention.

[0053] In Comparative Example No. 3, both the Ti content in the wire and the value calculated by formula (1) were below the lower limit of the range specified in the present invention, and therefore the rust prevention properties were poor.

[0054] As described above in detail, the gas-shielded arc welding wire according to the embodiment of the present invention generates little spatter during welding, does not require steps such as slag removal after welding, has excellent electrodeposition coatability, and can produce a weld with a good bead shape. [Explanation of symbols]

[0055] 1,2 Steel plate 3 Weld metal 4 welding torches 4a wire

Claims

1. Per total wire mass, Mn: 1.88% by mass or more and 2.70% by mass or less, Ti: 0.10% by mass or more and 0.30% by mass or less, O: more than 0.0050% by mass and not more than 0.0105% by mass, C: 0.01% by mass or more and 0.10% by mass or less, Si: 0.05% by mass or more and 0.50% by mass or less, Cu: 0.01% by mass or more and 0.30% by mass or less, S: 0.001% by mass or more and 0.020% by mass or less, Contains Al: 0.10% by mass or less, P: 0.025% by mass or less, The balance is Fe and unavoidable impurities, When the Ti content per total mass of the wire is expressed as [Ti] in mass% and the O content per total mass of the wire is expressed as [O] in mass%, A gas-shielded arc welding wire characterized in that a value calculated by the formula (1): 1000 × [Ti] × [O] / ([Ti] + 50 × [O]) is 2.13 or more and 3.50 or less.

2. The wire for gas-shielded arc welding according to claim 1, characterized in that the Si content is 0.25 mass % or less.

3. The wire for gas-shielded arc welding according to claim 1 or 2, characterized in that the Ti content is 0.15 mass % or more.

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