CN107848082B - Flux-cored wire for gas-shielded arc welding - Google Patents
Flux-cored wire for gas-shielded arc welding Download PDFInfo
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- CN107848082B CN107848082B CN201680041319.6A CN201680041319A CN107848082B CN 107848082 B CN107848082 B CN 107848082B CN 201680041319 A CN201680041319 A CN 201680041319A CN 107848082 B CN107848082 B CN 107848082B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/368—Selection of non-metallic compositions of core materials either alone or conjoint with selection of soldering or welding materials
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- Chemical & Material Sciences (AREA)
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- Nonmetallic Welding Materials (AREA)
Abstract
A flux-cored wire for gas shielded arc welding having a flux filled in a steel sheath, the flux-cored wire comprising a predetermined amount of BaF in the total mass of the wire2、C、Si、Mn、Al、Mg、Ni、Zr、Fe、Li，BaF2The value of the content of (b)/(the content of Al + the content of Zr) is 2.1 to 20.0.
Description
Technical Field
The present invention relates to a flux-cored wire for gas-shielded arc welding. More specifically, the present invention relates to a flux-cored wire for gas-shielded arc welding which is applicable to all-position welding including a vertical position.
Background
In the field of marine structures and pipeline, the sea area in which energy resources are being developed has been made deep, and resource exploration and mining areas for the extreme seas such as the arctic ocean have been expanded, and equipment has been made larger. Against the background of such a technical trend, in the design of marine structures and line pipes, the strength and toughness have been increased, and the performance requirements for welded joints have become more stringent.
On the other hand, flux-cored wires for all-position welding are required as welding materials from the viewpoint of high efficiency. In addition, the weld metal obtained also requires high fracture toughness.
However, in the flux-cored wire for the conventional all-position welding, since the amount of oxygen in the obtained weld metal is high, it is difficult to ensure low-temperature toughness of the welded joint portion when gas shielded arc welding is performed using the flux-cored wire.
Therefore, for example, patent document 1 discloses a flux-cored wire which can perform efficient welding in all postures and has excellent toughness.
[ Prior art documents ]
[ patent document ]
[ patent document 1 ] Japanese patent application laid-open No. 62-166098
However, in the technique disclosed in patent document 1, the strength of the weld metal is not of a high level (table 2 of patent document 1), and it is difficult to say that the properties required for structural materials in the marine structure field and the line pipe field are sufficiently satisfied at present. In addition, in patent document 1, the temperature for evaluation of impact properties (toughness) is high (table 2 of patent document 1), and the weld metal obtained by the technique disclosed in patent document 1 cannot be judged to be excellent in low-temperature toughness.
Further, flux-cored wires are required to have not only welding workability but also excellent 0.2% yield strength and hot crack resistance, and to be able to obtain weld metal having a small amount of diffusible hydrogen.
Disclosure of Invention
Accordingly, an object of the present invention is to provide a flux-cored wire for gas-shielded arc welding which is excellent in welding workability in all-posture welding such as an upright posture, and which is excellent in low-temperature toughness, 0.2% yield strength, tensile strength, and hot cracking resistance, and which can obtain a weld metal having a small amount of diffusible hydrogen.
In order to solve the above problems, the present invention proposes the following technical means.
The flux-cored wire for gas shielded arc welding of the present invention is a flux-cored wire for gas shielded arc welding having a flux filled in a steel sheath, and contains BaF in the total mass of the wire2: 2.0 to 11.1 mass%, C: 0.01 to 0.10 mass% of Si: 0.10 to 1.50 mass%, Mn: 0.70% by mass or more and 3.50% by mass or less, Al: 0.45% by mass or more and less than 2.00% by mass, Mg: 0.10 to 2.00 mass%, Ni: 0.50 to 12.00 mass% of Zr: 0.01 to 1.00 mass% inclusive, Fe: 70.0 to 90.0 mass% inclusive, Li: 0.01 to 1.00 mass% of the BaF2The value of the content of (b)/(the content of Al + the content of Zr) is 2.1 to 20.0.
According to the flux-cored wire, the content of the predetermined component is within the predetermined rangeAnd BaF2The value of (b)/(Al content + Zr content) is in a predetermined range, and therefore, the welding workability is excellent in all-posture welding including the upright posture, and the weld metal is excellent in low-temperature toughness, 0.2% yield strength, tensile strength and hot cracking resistance, and a weld metal with a small amount of diffusible hydrogen can be obtained.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain CaF in the total mass of the wire2: 2.0% by mass or less.
According to this flux cored wire, since CaF2The content of (b) is a predetermined value or less, and therefore, the welding wire can be obtained with a reliable effect of improving the welding workability.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain, in the total mass of the wire, metal oxides: 0.29% by mass or less.
According to this flux cored wire, since the content of the metal oxide is a predetermined value or less, it is possible to obtain a wire which ensures excellent low-temperature toughness of the weld metal.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain, in the total mass of the wire, a metal carbonate: 10.0% by mass or less.
According to this flux-cored wire, since the content of the metal carbonate is a predetermined value or less, it is possible to obtain a wire which ensures excellent low-temperature toughness of the weld metal.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain, in the total mass of the wire, Cr: 1.00 mass% or less, and Mo: 1.00 mass% or less.
According to this flux-cored wire, since the contents of Cr and Mo are equal to or less than predetermined values, it is possible to obtain a wire which has excellent strength and ensures the weld metal.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain, in the total mass of the wire, NaF: 1.00 mass% or less.
According to this flux-cored wire, since the content of NaF is equal to or less than a predetermined value, the effect of improving the welding workability can be reliably obtained.
The flux-cored wire for gas-shielded arc welding according to the present invention may contain, in the total mass of the wire, Ca: 1.00 mass% or less.
According to this flux-cored wire, since the content of Ca is equal to or less than a predetermined value, the effect of improving the welding workability can be reliably obtained.
The flux-cored wire for gas-shielded arc welding of the present invention may contain, in the total mass of the wire, Ce and La: the total amount is 0.300 mass% or less.
According to this flux-cored wire, since the total content of Ce and La is equal to or less than a predetermined value, it is possible to obtain a wire that ensures excellent low-temperature toughness of the weld metal.
The flux-cored wire for gas-shielded arc welding of the present invention is excellent in welding workability in all-posture welding including a vertical posture, and is excellent in low-temperature toughness, 0.2% yield strength, tensile strength, and hot crack resistance, and a weld metal with a small amount of diffusible hydrogen can be obtained.
Detailed Description
Hereinafter, the mode for carrying out the present invention will be described in detail.
The flux-cored wire for gas-shielded arc welding (hereinafter, referred to as "wire" or "flux-cored wire" as appropriate) of the present embodiment is a wire used for gas-shielded arc welding, and is a wire in which a flux is filled in a steel sheath.
Specifically, the welding wire of the present embodiment is composed of a cylindrical steel sheath and a flux filled inside the steel sheath. The welding wire may be of a seamless type having no seam on the outer steel sheath, or a seam type having a seam on the outer steel sheath. The wire may or may not be plated on the surface (outside the steel sheath).
The wire diameter (diameter) of the welding wire of the present embodiment is not particularly limited, and may be 1.2 to 2.4 mm. The flux filling rate of the welding wire is not particularly limited, but may be 12 to 25 mass% of the total mass of the welding wire from the viewpoint of wire drawability of the welding wire and workability (feedability and the like) at the time of welding.
In the welding wire of the present embodiment, the ratio of the content of each component to the total mass of the welding wire (steel sheath mass + flux mass) to the content of a predetermined component is specified.
The reason why the contents of the components of the welding wire of the present embodiment are specified will be described below.
[BaF2: 2.0 to 11.1 mass%]
BaF2Exhibits an effect as a strong deoxidizer and also exhibits an effect of a slag former which is excellent in the welding workability in all-posture welding. However, if BaF2When the content of (b) is less than 2.0 mass%, the bead shape cannot be ensured in welding in the upright posture, and the toughness deteriorates due to an increase in the amount of oxygen in the weld metal. On the other hand, if BaF2When the content of (b) is more than 11.1 mass%, the amount of diffusible hydrogen in the weld metal increases due to moisture absorption.
Thus, BaF2The content of (b) is 2.0 to 11.1 mass% based on the total mass of the wire.
In addition, from the viewpoint of further improving the above effect, BaF2The content of (b) is preferably 5.1% by mass or more, more preferably 6.0% by mass or more. In addition, BaF2The content of (b) is preferably 10.0% by mass or less, more preferably 9.0% by mass or less, from the viewpoint of suppressing an increase in the amount of diffusible hydrogen.
[ C: 0.01 to 0.10 mass% ]
C has an effect of improving the strength of the weld metal. However, if the content of C is less than 0.01 mass%, the yield strength and tensile strength of the weld metal are insufficient. On the other hand, if the content of C is more than 0.10 mass%, martensite is formed in an island shape in the weld metal, and toughness is deteriorated. Moreover, the strength of the weld metal is excessive, and cracks are likely to occur.
Therefore, the content of C is 0.01 mass% or more and 0.10 mass% or less in the total mass of the wire.
From the viewpoint of suppressing deterioration of toughness and from the viewpoint of suppressing occurrence of cracks, the content of C is preferably 0.08 mass% or less.
[ Si: 0.10 to 1.50 mass% ]
Si exerts an effect of promoting deoxidation of the weld metal. However, if the content of Si is less than 0.10 mass%, the deoxidation effect is lost, and the weld metal is subjected to blowholes. On the other hand, if the content of Si is more than 1.50 mass%, the viscosity of the weld metal increases, and fusion to the base metal deteriorates. Moreover, oxide inclusions are formed in the weld metal, and the toughness is deteriorated.
Therefore, the content of Si is 0.10 mass% or more and 1.50 mass% or less based on the total mass of the wire.
In addition, the content of Si is preferably 1.20 mass% or less from the viewpoint of suppressing a decrease in welding workability (suppressing a deterioration in fusion to the base material).
[ Mn: 0.70 to 3.50 mass% ]
Mn promotes deoxidation of the weld metal and exerts an effect of improving toughness of the weld metal. However, if the Mn content is less than 0.70 mass%, the deoxidation effect is insufficient, the weld metal is subjected to blowholes, and the toughness is deteriorated. On the other hand, if the Mn content is higher than 3.50 mass%, the strength of the weld metal becomes excessive, cracks easily occur, and the toughness deteriorates.
Therefore, the content of Mn is 0.70 mass% or more and 3.50 mass% or less in the total mass of the wire.
From the viewpoint of suppressing the occurrence of cracks and the viewpoint of suppressing the deterioration of toughness, the content of Mn is preferably 2.50 mass% or less.
[ Al: 0.45% by mass or more and less than 2.00% by mass ]
Al exerts an effect as a deoxidizer and adjusts molten BaF as a main component of the slag2The viscosity of (2) exerts an effect of finishing the bead shape in welding in a vertical posture. However, if the Al content is less than 0.45 mass%, the viscosity of the molten slag decreases, and weld metal occurs during welding in the vertical postureSagging of (2). Furthermore, Al in the solidified slag2O3The decrease in the phase results in easy breakage of the slag and deterioration of the slag removability. On the other hand, if the Al content is 2.00 mass% or more, coarse oxide inclusions are formed in the weld metal, and the toughness deteriorates.
Therefore, the content of Al is 0.45 mass% or more and less than 2.00 mass% in the total mass of the wire.
In addition, the content of Al is preferably 0.70 mass% or more from the viewpoint of suppressing a decrease in welding workability. From the viewpoint of suppressing deterioration of toughness, the content of Al is preferably 1.80 mass% or less.
[ Mg: 0.10 to 2.00 mass% ]
Mg exerts an effect of promoting deoxidation of the weld metal. However, if the Mg content is less than 0.10 mass%, the deoxidizing effect is insufficient, the weld metal is porous, and the toughness is deteriorated. On the other hand, if the Mg content is higher than 2.00 mass%, the solidification temperature of the molten slag decreases, and the welding workability in welding in the upright posture decreases.
Therefore, the content of Mg is 0.10 mass% or more and 2.00 mass% or less in the total mass of the wire.
From the viewpoint of suppressing deterioration of toughness, the content of Mg is preferably 0.50 mass% or more. In addition, the content of Mg is preferably 1.70 mass% or less from the viewpoint of suppressing a decrease in welding workability.
[ Ni: 0.50 to 12.00 mass% ]
Ni exerts an effect of improving toughness of the weld metal. However, if the Ni content is less than 0.50 mass%, the toughness of the weld metal is insufficient. On the other hand, if the Ni content is higher than 12.00 mass%, the possibility of occurrence of hot cracks in the weld metal is high.
Therefore, the content of Ni is 0.50 mass% or more and 12.00 mass% or less in the total mass of the wire.
From the viewpoint of suppressing deterioration of toughness, the content of Ni is preferably 1.00 mass% or more, and more preferably 2.00 mass% or more. From the viewpoint of suppressing the occurrence of thermal cracking, the content of Ni is preferably 9.00 mass% or less, and more preferably 5.00 mass% or less.
[ Zr: 0.01 to 1.00 mass% ]
Zr exerts an effect as a deoxidizer and adjusts molten BaF as a main component of the slag2The viscosity of (2) exerts an effect of finishing the bead shape in welding in a vertical posture. However, when the content of Zr is less than 0.01 mass%, the viscosity of the molten slag is lowered, and the weld metal sags during welding in the vertical posture. On the other hand, if the content of Zr is higher than 1.00 mass%, Zr melts in the weld metal, and the yield strength and tensile strength of the molten metal are significantly increased by solid solution strengthening. As a result, the toughness of the weld metal deteriorates.
Therefore, the content of Zr is 0.01 mass% or more and 1.00 mass% or less based on the total mass of the wire.
In addition, the content of Zr is preferably 0.05 mass% or more, and more preferably 0.10 mass% or more, from the viewpoint of suppressing a decrease in welding workability. From the viewpoint of suppressing deterioration of toughness, the content of Zr is preferably 0.90 mass% or less, and more preferably 0.80 mass% or less.
[ Fe: 70.0 to 90.0 mass% ]
Fe is the main component of the wire. If the content of Fe is less than 70.0 mass%, the deposited amount is insufficient. On the other hand, if the content of Fe is higher than 90.0 mass%, the relative amount of slag becomes insufficient, the toughness deteriorates due to insufficient deoxidation, and the bead shape becomes convex when welding is performed in a vertical posture.
Therefore, the content of Fe is 70.0 mass% or more and 90.0 mass% or less in the total mass of the wire.
[ Li: 0.01 to 1.00 mass% ]
Li exerts an effect of improving toughness of the weld metal. However, if the Li content is less than 0.01 mass%, Al and Zr excessively remain in the weld metal, and the yield strength and tensile strength of the weld metal are significantly increased. As a result, the toughness of the weld metal deteriorates. On the other hand, if the Li content is more than 1.00 mass%, the arc is unstable and unfused.
Therefore, the content of Li is 0.01 mass% or more and 1.00 mass% or less in the total mass of the wire.
From the viewpoint of suppressing occurrence of unfused fusion, the Li content is preferably 0.80 mass% or less, and more preferably 0.50 mass% or less.
[BaF2Content of (d)/(content of Al + content of Zr): 2.1 to 20.0 inclusive]
The welding wire of the present embodiment is characterized in that BaF is used2The ratio of the content of (b) to the total content of Al and Zr (═ BaF)2The value of the content of (b)/(the content of Al + the content of Zr) falls within a predetermined range.
As described, BaF2Exhibits an effect as a strong deoxidizer and also exhibits an effect as a slag former that excels in welding workability in all-posture welding, Al and Zr also exhibit an effect as deoxidizers, and molten BaF, which is a main component of slag, is adjusted2The viscosity of (2) exerts an effect of finishing the bead shape in welding in a vertical posture.
By setting the ratio of the content to a predetermined range, the effect of adjusting the bead shape to a preferable state is exhibited in welding in a vertical posture. However, if the ratio is less than 2.1, the volume of the molten slag is small, and the bead shape cannot be ensured in welding in the vertical posture. In addition, the oxygen content of the weld metal increases, and the toughness deteriorates. On the other hand, if the ratio is higher than 20.0, molten BaF, which is a main component of the slag2The viscosity of (2) is reduced, and the bead shape becomes convex in the welding in the vertical posture. Moreover, the volume of the slag becomes excessive, and slag inclusion occurs.
Thus, BaF2The value of the content of (b)/(the content of Al + the content of Zr) is 2.1 to 20.0.
From the viewpoint of preventing deterioration of toughness, the ratio is preferably 6.0 or more, and more preferably 7.0 or more. From the viewpoint of suppressing the reduction in welding workability, the ratio is preferably 15.0 or less, and more preferably 10.0 or less.
While the essential components of the welding wire of the present embodiment have been described so far, the following description will be made of optional components and inevitable impurities that the welding wire may contain in order to suppress the components contained in the welding wire and to obtain further effects.
[CaF2: 2.0 mass% or less]
CaF2Is a component to be suppressed in the wire, preferably CaF2The content of (b) is low (may be 0 mass%). And if CaF2The content of (b) is more than 2.0 mass%, and the viscosity of the molten slag is lowered, making welding in a vertical posture difficult.
Thus, CaF2When contained in the welding wire, CaF2The content of (b) is 2.0 mass% or less in the total mass of the wire.
[ metal oxide: 0.29% by mass or less ]
The metal oxide is a component to be contained in the wire, and is preferably contained in a low amount (may be 0 mass%). When the content of the metal oxide is more than 0.29 mass%, the metal oxide remains and disperses in the molten metal, and the low-temperature toughness of the weld metal deteriorates.
Therefore, when the metal oxide is contained in the wire, the content of the metal oxide is 0.29 mass% or less in the total mass of the wire.
The metal oxide is, in detail, Al2O3、Fe2O3、SiO2、TiO2The content of one or more of these metal oxides is the total content of the listed components.
[ metal carbonate: 10.0% by mass or less ]
The metal carbonate is a component to be contained in the wire, and is preferably contained in a low amount (may be 0 mass%). When the content of the metal carbonate is more than 10.0 mass%, the amount of oxygen in the weld metal increases, and the low-temperature toughness deteriorates. Further, the generation of excess gas causes a decrease in arc stability, which causes the occurrence of non-fusion.
Therefore, when the metal carbonate is contained in the wire, the content of the metal carbonate is 10.0 mass% or less in the total mass of the wire.
Also, the metal carbonate is, in detail, CaCO3、BaCO3The content of at least one of the metal carbonates is the total content of the respective components.
[ Cr: 1.00 mass% or less, Mo: 1.00% by mass or less ]
Neither Cr nor Mo is an essential component, but at least one of Cr and Mo contained in the wire exhibits an effect of improving the tensile strength of the weld metal. However, if the content of Cr is higher than 1.00 mass% or the content of Mo is higher than 1.00 mass%, the strength of the weld metal becomes excessive, and the possibility of occurrence of cracks becomes high. Moreover, the toughness of the weld metal deteriorates.
Therefore, when Cr and Mo are contained in the wire, Cr: 1.00 mass% or less and Mo: at least one of 1.00 mass% or less.
From the viewpoint of suppressing an excessive tensile strength and suppressing deterioration of toughness, the contents of Cr and Mo are preferably 0.30 mass% or less, respectively. From the viewpoint of further improving the above-described effects, the content of each of Cr and Mo is preferably 0.01 mass% or more, and more preferably 0.05 mass% or more.
[ NaF: 1.00% by mass or less ]
NaF is not an essential component, but is contained in the wire, thereby exhibiting an effect of improving welding workability. However, if the NaF content is higher than 1.00 mass%, the amount of diffusible hydrogen in the weld metal increases due to moisture absorption.
Therefore, if NaF is contained in the wire, the content of NaF is 1.00 mass% or less.
From the viewpoint of further improving the above effect, the content of NaF is preferably 0.01% by mass or more, and more preferably 0.05% by mass or more.
[ Ca: 1.00% by mass or less ]
Ca is not an essential component, but is contained in the wire, whereby the effect of improving welding workability is exhibited. However, if the content of Ca is more than 1.00 mass%, the molten slag is added as Ca oxide to reduce the viscosity of the slag, and the molten metal sags during welding in a vertical posture.
Therefore, Ca may be contained in the wire, and the content of Ca is 1.00 mass% or less.
From the viewpoint of further improving the above effect, the content of Ca is preferably 0.01 mass% or more, and more preferably 0.05 mass% or more.
[ Ce and La: 0.300% by mass or less in total ]
Ce. La is not an essential component, but when La is contained in the wire, the effect of improving toughness is exhibited. However, if the total content of Ce and La is more than 0.300 mass%, these components are oxidized to cause moisture adsorption, thereby suppressing an increase in the amount of diffusible hydrogen in the weld metal and lowering the low-temperature toughness.
Therefore, when Ce and La are contained in the wire, the total content of Ce and La is 0.300 mass% or less.
From the viewpoint of suppressing the increase in the amount of diffusible hydrogen, the total content of Ce and La is preferably 0.100 mass% or less. In addition, from the viewpoint of further improving the above effect, the content of the total of Ce and La is preferably 0.010 mass% or more.
[ balance: inevitable impurities ]
The balance of the composition of the welding wire of the present embodiment is inevitable impurities. Further, as inevitable impurities, P, S, Nb, V, Sb, Bi, B, and the like may be contained in a range not interfering with the effect of the present invention. In detail, P: 0.030% by mass or less, S: 0.030% by mass or less, Nb: 0.30 mass% or less, V: 0.30 mass% or less, Sb: 0.030% by mass or less, Bi: 0.0050 mass% or less, B: 0.0050% by mass or less.
In addition, if the balance is within a range not to impair the effects of the present invention, alloying agents such as Ti, Cu, Nb, V, Bi, and B, compounds thereof, arc stabilizers, and slag forming agents may be contained. When the components other than the metal oxide and the metal carbonate are added as an oxide and a nitride, the balance of the wire of the present embodiment naturally contains O and also N.
In addition, as the inevitable impurities, if the contents of P, S, Nb, V, Sb, Bi, B and the like exemplified are not more than the predetermined contents, the effects of the present invention are not hindered even when the inevitable impurities are positively added.
CaF having only the upper limit value defined2The metal oxide, the metal carbonate, Cr, Mo, NaF, Ca, Ce, and La may be positively added, but may be included as an inevitable impurity.
Although the components of the welding wire according to the present embodiment are described, the content of Al does not include Al derived from2O3Al of (4) does not contain Fe2O3Fe (b) does not contain Si derived from SiO2Si (B) does not contain C derived from a metal carbonate in terms of C content, and does not contain C derived from CaCO in terms of Ca content3、CaF2Ca of (2).
Next, a method for manufacturing a welding wire according to the present embodiment will be described.
[ method for producing welding wire ]
The method for manufacturing the welding wire according to the present embodiment is not particularly limited, and for example, the welding wire can be manufactured by the following method.
First, a steel strip constituting a steel outer skin is prepared, and the steel strip is formed by a forming roll while being fed in a longitudinal direction, thereby forming a U-shaped open pipe. Next, the respective components are blended so as to achieve a predetermined chemical composition, and the thus blended flux is filled in the steel sheath, and thereafter, processed so that the cross section becomes circular. Then, drawing is performed by cold working to obtain, for example, a flux-cored wire having a wire diameter of 1.2 to 2.4 mm. Further, annealing may be performed during cold working. Further, any configuration of a seamless welding wire in which a seam of a steel sheath formed in a manufacturing process is welded and a welding wire in which the seam is not welded and a gap is left as it is can be used.
[ examples ] A method for producing a compound
Hereinafter, examples of the present invention and comparative examples are given to specifically explain the effects of the present invention.
In the present example, flux-cored wires (diameter 1.6mm) of examples and comparative examples were produced by filling flux into a tubular sheath made of carbon steel having a composition within the range shown in table 1 below according to the production method. The balance of the outer skin components shown in table 1 below is Fe and inevitable impurities. In this case, the filling ratio of the flux is set to be in the range of 17.0 to 22.0 mass% in the total mass of the welding wire.
[ TABLE 1 ]
Tables 2 to 4 below show the total composition of the welding wires of examples and comparative examples. The balance of the wire components shown in tables 2 to 4 below is inevitable impurities.
In addition, "BaF" in tables 2 to 42/(Al + Zr) ", means" BaF2Content of (d)/(content of Al + content of Zr) ". In tables 2 to 4, "Ce or La" means "the total content of Ce and La".
In tables 2 to 4, the numeric values which do not satisfy the scope of the present invention are underlined.
[ TABLE 2 ]
[ TABLE 3 ]
[ TABLE 4 ]
Next, gas shielded arc welding was performed on the base materials shown in table 5 below using the flux-cored wires of examples and comparative examples. The balance of the base material composition shown in table 5 below is Fe and inevitable impurities.
[ TABLE 5 ]
The welding conditions were as follows.
Protective gas: 100% by volume CO225 l/min
Wire diameter: phi 1.6mm
Groove shape: 20 degree
Root spacing: 16mm
Welding current: 260A
Arc voltage: 26V
Welding posture: downwards facing
Welding speed: 250 mm/min
Welding line energy: 1.8kJ/mm
Welding length: 400mm
Preheating temperature: 100 to 110 DEG C
Interlayer temperature: 140-160 deg.C
Polarity: direct Current Electrode Negative (DCEN)
Then, the weld metal obtained by gas shielded arc welding using each of the flux-cored wires of examples and comparative examples was evaluated for mechanical properties (low-temperature toughness, 0.2% yield strength, tensile strength), diffusible hydrogen content, hot crack resistance, non-fusion, and occurrence of blowholes by the methods shown below.
< mechanical Properties >
Mechanical properties of the weld metal were determined by the following method in accordance with JIS Z3111: the tensile test and the impact test of "method of tensile and impact test of deposited metal" specified in 2005 were evaluated. As a result, the impact value at-80 ℃ (CVN-80) was 100J or more, which was acceptable for low temperature toughness. The 0.2% yield strength (0.2% PS) was not less than 690 MPa. The Tensile Strength (TS) is in the range of 770MPa to 930 MPa.
< diffusible Hydrogen quantity >
The amount of diffusible hydrogen in the weld metal was evaluated according to JIS Z3118: the method of 2007.
As a result, the amount of diffusible hydrogen ([ H ]]d) The content of the polymer in the sample was 8.0mL/100g or less.
< resistance to thermal cracking, no fusion, pores >
Evaluation of hot cracking resistance and non-fusion based on JIS Z3104: the "test method for radiation transmission of welded steel joint (original: hand)" as defined in 1995 was conducted.
After the completion of the welding, the occurrence of non-fusion, thermal cracking and blowholes in the welded part (the welded length: 400mm, except for the crater part) was confirmed by an X-ray transmission test, and the total length of the generated part was measured. Then, if the value calculated by (total length of the portion where no fusion, thermal cracking, or blowholes occur)/length of the welded portion × 100 is 0%, it is evaluated as "o", if it is higher than 0% and not higher than 5%, it is evaluated as "Δ", if it is higher than 5%, it is evaluated as "x", and if it is multiplied, it is evaluated that welding cannot be performed. Then, the results of O and Δ were passed. Also, what the welding itself cannot be performed is "-".
Further, with respect to each of the flux-cored wires of examples and comparative examples, the welding workability was evaluated by the following method.
< welding operability >
Regarding the welding workability, the base material shown in table 5 was fillet-welded in an upright position by using an automatic welding apparatus, and the evaluation was made based on the fusion between the base material and the weld bead and the cross-sectional shape of the weld bead. As a result, the welding was able to be performed in the upright position, and the welding bead surface after welding was smooth, and the welding was able to be performed in the upright position, but the welding bead surface after welding was a Δ when unevenness occurred, and the welding was not able to be performed by welding slag or molten metal sagging, or the welding bead surface was significantly recessed due to insufficient deposition, and the welding was x. Then, the results of O and Δ were passed.
Further, the slag removability was also evaluated.
Regarding the slag removability, the slag removability was evaluated as not allowing welding when the boundary portion (welding length: 400mm) between the slag and the base material was once struck with a chisel (FCH-20 by a non-binary mechanism, air pressure: 0.5MPa), and when there was slag removability of 70% or more, Δ was observed when slag removability of 50% or more and less than 70% was observed, and x was observed when slag removability of less than 50% was observed, relative to the length of the struck portion. Then, the results of O and Δ were passed.
The detailed welding conditions for evaluating the welding workability are as follows.
Parent material: base metal shown in Table 5
Welding current: 220A of
Arc voltage: 24V
Welding speed: 110 mm/min
Projection length: 20mm
Yaw width: 5mm
Automatic welding apparatus: PICOMAX-2Z made of Shenhu Steel
The above results are shown in tables 6 to 8 below. In tables 6 to 8, the numerical values which do not satisfy the evaluation criteria are underlined.
[ TABLE 6 ]
[ TABLE 7 ]
[ TABLE 8 ]
As shown in tables 6 and 7, Nos. 1 to 51 satisfying the specific matters of the present invention were all good in all the evaluation items.
On the other hand, as shown in table 8, nos. 52 to 81 did not satisfy the specific matters of the present invention, and therefore, were poor results in a certain evaluation item. In detail, the following is described.
No.52 because of BaF2Is less than the lower limit value, and the ratio (═ BaF)2The value of (a)/(the content of Al + the content of Zr) is lower than the lower limit value, so toughness deteriorates and upward fillet welding cannot be performed.
No.53 is because of BaF2The content of (b) is higher than the upper limit, so that the diffusible hydrogen content is large.
No.54 has low values of yield strength and tensile strength because the content of C is lower than the lower limit value.
Since the content of C in No.55 is higher than the upper limit, the strength is excessive and the toughness is deteriorated.
In sample No.56, the Si content was less than the lower limit, and therefore, blistering occurred.
Since the content of Si in No.57 is higher than the upper limit, the bead shape is poor, the welding workability is poor, and the toughness is deteriorated.
In sample No.58, Mn content is less than the lower limit, so that blowholes occur and toughness deteriorates.
In No.59, since the Mn content is higher than the upper limit, the strength is excessive and the toughness is deteriorated.
Since the content of Al is less than the lower limit value, No.60 has a poor bead shape, poor welding workability, and poor slag removability.
Since the content of Al was higher than the upper limit, No.61 had a slightly convex bead shape and deteriorated toughness.
No.62 was inferior in toughness because the Mg content was lower than the lower limit value, and blowholes occurred.
No.63 because the content of Mg is higher than the upper limit value, the weld metal droops in the vertical fillet welding and cannot be welded.
No.64 has poor toughness because the Ni content is less than the lower limit.
No.65 has thermal cracking because the Ni content is higher than the upper limit.
No.66 was unable to be welded because the weld metal sagged in the vertical fillet welding because the Zr content was lower than the lower limit value.
Since the content of Zr in No.67 was higher than the upper limit, the bead shape was slightly convex, the strength was excessive, and the toughness was deteriorated.
Since No.68 contained Fe at a level lower than the lower limit value, the amount of deposit was insufficient, and the bead shape was concave.
No.69, because the content of Fe was higher than the upper limit value, toughness deteriorated and upward fillet welding could not be performed.
In sample No.70, since the Li content is less than the lower limit, the strength is excessive and the toughness is deteriorated.
No.71 was not fused because the content of Li was higher than the upper limit.
No.72 cause ratio (═ BaF)2The value of (Al content + Zr content) is lower than the lower limit value), the bead shape is poor, the welding workability is poor, and the toughness is deteriorated.
No.73 cause ratio (═ BaF)2The value of (b)/(Al content + Zr content) is higher than the upper limit value, slag inclusion occurs, so that non-fusion occurs, and the bead shape is convex.
No.74 is due to CaF2The content of (B) is higher than the upper limit value, so that the upward vertical fillet welding cannot be performed.
No.75 had deteriorated toughness because the content of the metal oxide was higher than the upper limit.
No.76 was not fused and the toughness was deteriorated because the content of the metal carbonate was higher than the upper limit value.
No.77 has an excessive strength and deteriorated toughness because the Cr content is higher than the upper limit.
In No.78, the content of Mo is higher than the upper limit, so that the strength is excessive and the toughness is deteriorated.
In No.79, the content of NaF was higher than the upper limit, and therefore the diffusible hydrogen content was large.
No.80 is difficult to fillet weld in the vertical direction because the content of Ca is higher than the upper limit.
In sample No.81, the total content of Ce and La was higher than the upper limit, so that the diffusible hydrogen content was large.
While the present invention has been described in detail with reference to the embodiments and examples, the spirit of the present invention is not limited to the above description, and the scope of the claims should be construed broadly based on the description of the scope of the patent claims. It is needless to say that the contents of the present invention may be changed or modified based on the description.
This application is based on japanese patent application (patent application 2015-143365) filed on 7/17/2015, the contents of which are incorporated herein by reference.
[ industrial applicability ]
The flux-cored wire for gas-shielded arc welding of the present invention is particularly useful for welding structures in the marine structure field and the line pipe field.
Claims (1)
1. A flux-cored wire for gas shielded arc welding, characterized in that a flux is filled in a steel sheath,
the total mass of the welding wire comprises:
BaF2: 5.1 to 11.1 mass%;
c: 0.01 to 0.10 mass%;
si: 0.10 mass% or more and 1.50 mass% or less;
mn: 0.70 to 3.50 mass%;
al: 0.45 mass% or more and less than 2.00 mass%;
mg: 0.10 mass% or more and 2.00 mass% or less;
ni: 0.50 to 12.00 mass%;
zr: 0.01 to 1.00 mass%;
fe: 70.0 to 90.0 mass%;
li: 0.01 to 1.00 mass% inclusive,
the BaF2The value of (b)/(the Al content + the Zr content) is 4.7 to 20.0,
and at least 1 of the following (a) to (g):
(a) of the total mass of the welding wire, CaF2: 2.0% by mass or less;
(b) in the total mass of the welding wire, the ratio of metal oxide: 0.29% by mass or less;
(c) in the total mass of the welding wire, the metal carbonate: 10.0% by mass or less;
(d) in the total mass of the welding wire, Cr: 1.00 mass% or less, and Mo: 1.00 mass% or less;
(e) in the total mass of the welding wire, NaF: 1.00 mass% or less;
(f) in the total mass of the welding wire, Ca: 1.00 mass% or less;
(g) in the total mass of the wire, Ce and La: the total amount is 0.300 mass% or less.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015143365A JP6453178B2 (en) | 2015-07-17 | 2015-07-17 | Flux-cored wire for gas shielded arc welding |
| JP2015-143365 | 2015-07-17 | ||
| PCT/JP2016/067602 WO2017013965A1 (en) | 2015-07-17 | 2016-06-14 | Wire containing flux for gas shield arc welding |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107848082A CN107848082A (en) | 2018-03-27 |
| CN107848082B true CN107848082B (en) | 2020-09-04 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201680041319.6A Active CN107848082B (en) | 2015-07-17 | 2016-06-14 | Flux-cored wire for gas-shielded arc welding |
Country Status (5)
| Country | Link |
|---|---|
| JP (1) | JP6453178B2 (en) |
| KR (1) | KR102011608B1 (en) |
| CN (1) | CN107848082B (en) |
| SG (1) | SG11201800258QA (en) |
| WO (1) | WO2017013965A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2019171457A (en) * | 2018-03-29 | 2019-10-10 | 株式会社神戸製鋼所 | Flux-cored wire for high speed welding and high speed arc welding method |
| JP7231477B2 (en) * | 2019-05-09 | 2023-03-01 | 株式会社神戸製鋼所 | FLUX CORE WIRE, WELDING METHOD AND WELD METAL |
| JP7231476B2 (en) * | 2019-05-09 | 2023-03-01 | 株式会社神戸製鋼所 | FLUX CORE WIRE, WELDING METHOD AND WELD METAL |
| JP7231499B2 (en) * | 2019-06-20 | 2023-03-01 | 株式会社神戸製鋼所 | Flux-cored wire and welding method |
| CN111571063B (en) * | 2020-06-24 | 2022-04-15 | 北京金威焊材有限公司 | Flux-cored wire for ultralow-temperature stainless steel welding |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20060096966A1 (en) * | 2004-11-08 | 2006-05-11 | Lincoln Global, Inc. | Self-shielded flux cored electrode for fracture critical applications |
| JP5097499B2 (en) * | 2006-10-19 | 2012-12-12 | 株式会社神戸製鋼所 | Flux-cored wire for gas shielded arc welding for low alloy heat resistant steel |
| JP4834191B2 (en) * | 2009-12-16 | 2011-12-14 | 新日本製鐵株式会社 | Flux-cored wire for gas shielded arc welding that can be welded in all positions |
| JP5880662B2 (en) | 2013-11-08 | 2016-03-09 | 新日鐵住金株式会社 | Flux-cored wire for gas shielded arc welding, welding method of steel for cryogenic temperature, and manufacturing method of welded joint |
| JP2016187828A (en) * | 2015-03-30 | 2016-11-04 | 株式会社神戸製鋼所 | Flux-cored wire for gas shield arc welding |
-
2015
- 2015-07-17 JP JP2015143365A patent/JP6453178B2/en active Active
-
2016
- 2016-06-14 KR KR1020187000855A patent/KR102011608B1/en active IP Right Grant
- 2016-06-14 WO PCT/JP2016/067602 patent/WO2017013965A1/en active Application Filing
- 2016-06-14 SG SG11201800258QA patent/SG11201800258QA/en unknown
- 2016-06-14 CN CN201680041319.6A patent/CN107848082B/en active Active
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| JPS62166098A (en) * | 1986-01-14 | 1987-07-22 | Nippon Steel Corp | Flux-cored wire for gas shielded arc welding |
| CN1209376A (en) * | 1997-08-22 | 1999-03-03 | 株式会社神户制钢所 | Coat core-wire for gas-protection arc welding |
| JPH11207491A (en) * | 1998-01-26 | 1999-08-03 | Kobe Steel Ltd | Flux cored wire for co2 gas shielded arc welding using dc straight polarity and welding method thereof |
| CN100553856C (en) * | 2006-10-19 | 2009-10-28 | 株式会社神户制钢所 | Flux-cored wire for gas shielded arc welding for creep-resisting steels |
| CN101185996A (en) * | 2006-11-20 | 2008-05-28 | 株式会社神户制钢所 | Flux-cored wire for electrogas welding and electrogas welding metal |
| CN102139420A (en) * | 2010-02-02 | 2011-08-03 | 株式会社神户制钢所 | Flux-cored wire |
| CN104271310A (en) * | 2012-05-08 | 2015-01-07 | 新日铁住金株式会社 | Flux-containing wire for welding ultrahigh-tensile steel |
| WO2015083878A1 (en) * | 2013-12-06 | 2015-06-11 | 주식회사 포스코 | High-strength welding joint having excellent cryogenic impact toughness, and wire for flux-cored arc welding therefor |
Also Published As
| Publication number | Publication date |
|---|---|
| KR20180016569A (en) | 2018-02-14 |
| WO2017013965A1 (en) | 2017-01-26 |
| KR102011608B1 (en) | 2019-08-16 |
| JP6453178B2 (en) | 2019-01-16 |
| JP2017024032A (en) | 2017-02-02 |
| SG11201800258QA (en) | 2018-02-27 |
| CN107848082A (en) | 2018-03-27 |
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