WO2023032932A1 - サブマージアーク溶接方法 - Google Patents

サブマージアーク溶接方法 Download PDF

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Publication number
WO2023032932A1
WO2023032932A1 PCT/JP2022/032458 JP2022032458W WO2023032932A1 WO 2023032932 A1 WO2023032932 A1 WO 2023032932A1 JP 2022032458 W JP2022032458 W JP 2022032458W WO 2023032932 A1 WO2023032932 A1 WO 2023032932A1
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welding
submerged arc
arc welding
steel
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PCT/JP2022/032458
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English (en)
French (fr)
Japanese (ja)
Inventor
彰芳 安藤
充志 ▲高▼田
一史 渡邊
能知 岡部
圭治 植田
正道 鈴木
鵬 韓
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JFE Steel Corp
Kobe Steel Ltd
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JFE Steel Corp
Kobe Steel Ltd
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Priority to EP22864514.9A priority Critical patent/EP4365326A4/en
Priority to US18/293,892 priority patent/US20250065432A1/en
Priority to CN202280057416.XA priority patent/CN117836088A/zh
Priority to KR1020247004414A priority patent/KR20240032963A/ko
Priority to JP2023504451A priority patent/JP7267521B1/ja
Publication of WO2023032932A1 publication Critical patent/WO2023032932A1/ja
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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
    • B23K9/00—Arc welding or cutting
    • B23K9/18—Submerged-arc welding
    • 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
    • B23K9/00—Arc welding or cutting
    • B23K9/18—Submerged-arc welding
    • B23K9/186—Submerged-arc welding making use of a consumable electrodes
    • 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 or wires
    • 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 or wires
    • B23K35/0266—Rods, electrodes or wires flux-cored
    • 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°C
    • 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°C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/3073—Fe as the principal constituent with Mn as next major constituent
    • 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°C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/308—Fe as the principal constituent with Cr as next major constituent
    • 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 or fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • 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 or fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/3601—Selection of non-metallic compositions, e.g. coatings or fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest with inorganic compounds as principal constituents
    • B23K35/3602—Carbonates, basic oxides or hydroxides
    • 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 or fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/362—Selection of compositions of fluxes
    • 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 or 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
    • 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
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • 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
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • 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
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
    • 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys

Definitions

  • the present invention relates to a submerged arc welding method, and more particularly to a welding material suitable for welding high Mn-containing steel materials used in an extremely low temperature environment and a submerged arc welding method using the same.
  • LNG liquefied natural gas
  • containers for transporting or storing LNG are required to retain excellent cryogenic impact toughness at temperatures below -162°C, which is the liquefaction temperature of LNG.
  • aluminum alloys, 9% Ni steels, austenitic stainless steels, etc. have conventionally been used as materials for containers and the like due to the need to maintain excellent cryogenic impact toughness.
  • high Mn-containing steel materials containing Mn in the range of 10 to 35% by mass have been used as materials for containers for transporting or storing LNG.
  • High-Mn steel has an austenitic phase metal structure even at extremely low temperatures, does not cause brittle fracture, and has a higher strength than austenitic stainless steel. Therefore, there has been a demand for development of a stable welding method for such high-Mn steel.
  • Patent Document 1 discloses, in mass %, C: 0.2 to 0.8%, Si: 0.15 to 0.90%, Mn: 17.0 to 28.0%. 0%, P: 0.03% or less, S: 0.03% or less, Ni: 0.01 to 10.00%, Cr: 0.4 to 4.0%, Mo: 0.01 to 3.50 %, B: less than 0.0010%, N: 0.12% or less, the balance has a basic composition consisting of Fe and inevitable impurities, and is selected from V, Ti and Nb as necessary Disclosed is a solid wire for gas metal arc welding containing one or more, and one or more selected from Cu, Al, Ca and REM.
  • the amount of fume generation is small, and the yield strength at room temperature (0.2% yield strength) is high strength of 400 MPa or more, and the test temperature: - It is said that it is possible to produce welded joints with high strength and excellent cryogenic impact toughness such that the absorbed energy (vE ⁇ 196 ) in a Charpy impact test at 196° C. is 28 J or more.
  • Patent Document 1 can suppress the amount of fume generated during welding to 1200 mg/min or less, but the welding heat input is increased in order to increase the welding efficiency. There is a problem that the amount of generated fume is proportional to the increase. In order to solve this problem, submerged arc welding, which generates less fume, is used. Although the amount of fume generated can be suppressed, there are problems such as irregular bead shape, poor slag peelability, and deterioration of yield strength and low temperature toughness. It was found that
  • the present invention solves the above-described problems of the conventional technology, generates an extremely small amount of fume during welding even under welding conditions with a high heat input (3 kJ/mm or more), and has good weldability such as bead shape and slag peelability.
  • the object of the present invention is to provide a submerged arc welding method capable of obtaining a weld metal having both high strength and excellent cryogenic toughness, which is suitable as a welding material for high Mn content steel used in cryogenic environments. do.
  • the amount of fume generated during welding is small refers to the case where the amount of fume generated when performing submerged arc welding is 1200 mg/min or less in accordance with JIS Z 3930-2013.
  • High strength refers to the case where the room-temperature yield strength (0.2% proof stress) of the weld metal manufactured in accordance with JIS Z 3111 is 400 MPa or more.
  • Excellent cryogenic toughness means that the absorbed energy (vE -196 ) of the weld metal manufactured in accordance with JIS Z 3111 in the Charpy impact test at -196°C is 28 J or more. point to
  • the present inventors firstly controlled the flux composition in order to obtain an appropriate bead shape, good slag releasability, and good weld metal properties in submerged arc welding. I found that it is effective. As a result of repeated studies on the flux component, it was found that welding using a flux with a basicity [BL] of 1.5 to 2.4 can suppress poor slag separation, irregular bead shape, and deterioration of low temperature toughness. .
  • the yield strength may decrease depending on the plate thickness of the material to be welded, the shape of the groove, and the welding conditions, even if the welding wire and flux described above are used. Therefore, the present inventors have further studied and found that determining the welding conditions by controlling the welding heat input with respect to the cross-sectional area of the groove to an appropriate range is effective in preventing a decrease in yield strength. bottom.
  • the present invention was completed based on these findings and further studies, and the gist of the present invention is as follows. [1] % by mass, C: 0.20 to 0.80%, Si: 0.15 to 0.90%, Mn: 17.0 to 28.0%, P: 0.030% or less, S: 0.030% or less, Ni: 0.01 to 10.00%, Cr: 0.4 to 4.0%, Mo: 0.01 to 3.50%, N: 0.120% or less, the balance
  • a submerged arc welding wire having a composition consisting of Fe and unavoidable impurities and a flux having a basicity [BL] defined by the following formula (1): 1.5 to 2.4 are combined to obtain the following formula (2)
  • a submerged arc welding method characterized by welding with a welding heat input [Q] that satisfies.
  • BL (%CaO+%MgO+%BaO+%SrO+% Na2O +% K2O +% Li2O +% CaF2 +0.5%MnO+0.5%FeO)/(% SiO2 +0.5% Al2O3 + 0 .5% TiO 2 +0.5% ZrO 2 ) (1)
  • the amount of each component in the formula (1) is the amount of the component expressed in mass%.
  • Q [J / mm] I [A] ⁇ E [V] ⁇ 60 / V [mm / min], I ⁇ 300 [A], E ⁇ 15 [V], and V ⁇ 100 [mm/min].
  • the composition further contains, in % by mass, one selected from V: 0.040% or less, Ti: 0.040% or less, and Nb: 0.040% or less, or A submerged arc welding method containing two or more.
  • the composition is further selected from Cu: 1.00% or less, Ca: 0.010% or less, and REM: 0.020% or less in mass%.
  • a submerged arc welding method containing one or more.
  • the steel material to be welded contains, in mass%, C: 0.20 to 0.80%, Si: 0.15 to 0.90%. , Mn: 15.0 to 30.0%, P: 0.030% or less, S: 0.030% or less, Ni: 3.00% or less, Cr: 1.0 to 8.0%, the balance
  • the steel material further contains, by mass%, V: 2.00% or less, Ti: 1.00% or less, Nb: 1.00% or less, and Al: 0.100% or less, Cu: 1.00% or less, N: 0.120% or less, O (oxygen): 0.0050% or less, B: 0.0030% or less, and REM: 0.0200% or less
  • V 2.00% or less
  • Ti 1.00% or less
  • Nb 1.00% or less
  • Al 0.100% or less
  • Cu 1.00% or less
  • N 0.120% or less
  • B 0.0030% or less
  • REM 0.0200% or less
  • a submerged arc welding method containing one or more selected from.
  • the present invention it is possible to provide a welding material for high Mn-containing steel material that can remarkably suppress the amount of fume generated during submerged arc welding and has good bead shape and slag releasability.
  • the room temperature yield strength (0.2% yield strength) is 400 MPa or more
  • the test temperature is -196 ° C. Absorbed energy (vE -196 ) is 28 J or more, a weld metal having high strength and excellent cryogenic toughness can be easily obtained.
  • INDUSTRIAL APPLICABILITY The present invention can provide the welding material and the submerged arc welding method using the same, and has a remarkable industrial effect.
  • FIG. 4 is a correlation diagram showing the relationship between groove cross-sectional area and welding heat input in submerged arc welding.
  • the present invention relates to a submerged arc welding method using specific welding consumables, particularly for steels with high Mn content.
  • SAW submerged arc welding
  • SAW is a welding method in which an electrode wire is continuously supplied in powdery flux that has been pre-dispersed on the base material, and an arc is generated between the tip of the electrode wire and the base material for continuous welding. is.
  • This SAW has the advantage of being able to weld efficiently by applying a high current to increase the deposition rate of the wire.
  • the electrode wire includes a solid wire or a flux-cored wire in which flux for wire is contained inside the wire, either of which can be used in the present invention.
  • a flux-cored wire is used, the component composition of the steel sheath, the metal powder, and the wire-use flux powder is adjusted before the flux-cored wire is produced.
  • Examples of submerged arc welding according to the present invention include the following. Two steel materials to be welded are butted against each other to form a 45° V groove, and flux is spread in advance so as to cover the formed groove. Using the prepared solid wire (diameter 4.0 mm ⁇ ) or flux cored wire (diameter 3.2 mm ⁇ ), in a downward position, current: 350 to 650 A (DCEP), voltage: 28 to 36 V, welding speed: 20 to 80 cm /min, welding heat input: 0.7 to 8.0 kJ/mm, and interpass temperature: 100 to 150°C.
  • the high-Mn steel that serves as the base material is butted together, and a welding flux and submerged arc welding wire, which will be described later, are used to produce the weld metal that forms the welded joint.
  • C is an element that has the effect of increasing the strength of the weld metal by solid-solution strengthening, and C stabilizes the austenite phase and improves the cryogenic impact toughness of the weld metal.
  • the content 0.20% or more is required.
  • carbide precipitates, the cryogenic toughness is lowered, and hot cracks are likely to occur during welding. Therefore, C is limited to the range of 0.20 to 0.80%.
  • the content is preferably 0.30% or more and 0.70% or less, and more preferably 0.40% or more and 0.60% or less. More preferably, it is 0.45% or more and 0.55% or less.
  • Si acts as a deoxidizing agent, increases the yield of Mn, increases the viscosity of the molten metal, stably maintains the bead shape, and has the effect of reducing the occurrence of spatter.
  • the content of 0.15% or more is required.
  • the cryogenic toughness of the weld metal is lowered.
  • Si segregates during solidification to form a liquid phase at solidification cell interfaces, thereby deteriorating hot cracking resistance. Therefore, Si is limited to the range of 0.15 to 0.90%.
  • the content is preferably 0.20% or more and 0.80% or less, more preferably 0.25% or more and 0.70% or less. It is more preferably 0.30% or more and 0.65% or less, and even more preferably 0.40% or more and 0.60% or less.
  • Mn is an element that stabilizes the austenite phase at low cost, and the present invention requires a content of 17.0% or more. If the Mn content is less than 17.0%, a ferrite phase is formed in the weld metal and the toughness at cryogenic temperatures is significantly lowered. On the other hand, when Mn exceeds 28.0%, excessive Mn segregation occurs during solidification, which induces hot cracking. Therefore, Mn is limited to the range of 17.0 to 28.0%. In addition, it is preferably 18.0% or more and 27.0% or less, and more preferably 19.0% or more and 26.0% or less. More preferably, it is 20.0% or more and 24.0% or less.
  • P is an element that segregates at grain boundaries and induces hot cracking. In the present invention, it is preferable to reduce P as much as possible, but if it is 0.030% or less, it is permissible. Therefore, P is limited to 0.030% or less. In addition, excessive reduction causes a rise in refining cost. Therefore, P is preferably adjusted to 0.003% or more. More preferably, it is 0.005% or more and 0.020% or less, and still more preferably 0.009% or more and 0.016% or less.
  • S exists as sulfide inclusions MnS in the weld metal. Since MnS serves as a starting point for fracture generation, it lowers the cryogenic toughness. Therefore, S is limited to 0.030% or less. In addition, excessive reduction causes a rise in refining cost. Therefore, S is preferably adjusted to 0.001% or more. More preferably, it is 0.008% or more and 0.025% or less, and still more preferably 0.013% or more and 0.020% or less.
  • Ni is an element that strengthens austenite grain boundaries, segregates at grain boundaries, and improves cryogenic impact toughness. In order to obtain such an effect, the content of 0.01% or more is required. In addition, Ni also has the effect of stabilizing the austenite phase, so if the content is further increased, the austenite phase is stabilized and the cryogenic impact toughness of the weld metal is improved. However, Ni is an expensive element, and a content exceeding 10.00% is economically disadvantageous. Therefore, Ni is limited to 0.01 to 10.00%. The content is preferably 0.05% or more and 7.5% or less, and more preferably 1.00% or more and 4.00% or less. More preferably, it is 1.50% or more and 2.50% or less.
  • Cr acts as an element that stabilizes the austenite phase at cryogenic temperatures and improves the cryogenic impact toughness of the weld metal. Cr also has the effect of improving the strength of the weld metal. Moreover, Cr raises the liquidus line of the molten metal and acts effectively to suppress the occurrence of hot cracks. Furthermore, Cr also effectively acts to improve the corrosion resistance of the weld metal. In order to obtain such an effect, the content of 0.4% or more is required. If Cr is less than 0.4%, the above effects cannot be secured. On the other hand, when the Cr content exceeds 4.0%, Cr carbides are formed, leading to a decrease in cryogenic toughness. Furthermore, the formation of carbides lowers workability during wire drawing. Therefore, Cr is limited to the range of 0.4 to 4.0%. The content is preferably 0.5% or more and 3.5% or less, and more preferably 0.8% or more and 3.0% or less. More preferably, it is 1.0% or more and 2.0% or less.
  • Mo 0.01 to 3.50%
  • Mo is an element that strengthens the austenite grain boundaries, segregates at the grain boundaries, and improves the strength of the weld metal. Such an effect becomes remarkable at a content of 0.01% or more.
  • the content exceeds 0.01%, it also has the effect of improving the strength of the weld metal by solid solution strengthening.
  • Mo is limited to the range of 0.01 to 3.50%.
  • it is 0.50% or more and 3.00% or less. It is more preferably 1.00% or more and 2.80% or less, and still more preferably 1.50% or more and 2.20% or less.
  • N is an element that is unavoidably mixed, but like C, it is an element that effectively contributes to improving the strength of the weld metal, stabilizes the austenite phase, and stably improves the cryogenic toughness. Since such an effect becomes remarkable at a content of 0.030% or more, a content of 0.030% or more is preferable. However, if the content exceeds 0.120%, nitrides are formed and the low temperature toughness is lowered. Therefore, N is limited to 0.120% or less. Preferably, it is 0.030 to 0.120%. More preferably, it is 0.060% or more and 0.100% or less.
  • the composition described above is the basic composition for the wire of the present invention.
  • V 0.040% or less
  • Ti 0.040% or less
  • Nb 0.040% or less
  • An optional composition containing one or more of these may be used.
  • the basic composition and the optionally selected composition are further optionally selected from Cu: 1.00% or less, Ca: 0.010% or less, and REM: 0.020% or less. It can contain more than one species.
  • V, Ti, and Nb are elements that promote the formation of carbides and contribute to improving the strength of the weld metal, and one or more of them can be selected as necessary.
  • V is a carbide-forming element that precipitates fine carbides and contributes to improving the strength of the weld metal. In order to obtain such effects, it is preferable to contain 0.001% or more. However, if the content exceeds 0.040%, the carbides become coarse and the cryogenic toughness is lowered. Therefore, when it is contained, V is preferably 0.040% or less. More preferably, it is 0.001 to 0.040%. More preferably, it is 0.020% or more.
  • Ti is also a carbide-forming element, precipitates fine carbides, and contributes to improving the strength of the weld metal.
  • Ti precipitates carbides on solidification cell interfaces of the weld metal, and contributes to suppressing the occurrence of hot cracks.
  • it is preferable to contain 0.001% or more.
  • the content exceeds 0.040%, the carbides become coarse like V, leading to a decrease in cryogenic toughness. Therefore, when Ti is contained, it is preferable that Ti is 0.040% or less. More preferably, it is 0.001 to 0.040%. More preferably, it is 0.020% or more.
  • Nb is also a carbide-forming element, precipitates fine carbides, and contributes to improving the strength of the weld metal.
  • Nb precipitates carbides on solidification cell interfaces of the weld metal and contributes to suppression of hot cracking.
  • it is preferable to contain 0.001% or more.
  • Nb is preferably 0.040% or less. More preferably, it is 0.001 to 0.040%. More preferably, it is 0.005% or more.
  • Cu is an element that contributes to stabilizing austenite
  • Ca and REM are elements that contribute to improving workability. The reasons for the limitations are described below.
  • Cu is an element that stabilizes the austenite phase, and stabilizes the austenite phase even at cryogenic temperatures, thereby improving the cryogenic impact toughness of the weld metal.
  • it is preferable to contain 0.01% or more. However, if the content exceeds 1.00% and is large, the hot ductility is lowered. Therefore, when it is contained, Cu is preferably 1.00% or less. More preferably, it is 0.01 to 1.00%. More preferably, it is 0.05% or more and 0.60% or less.
  • Ca 0.010% or less
  • Ca combines with S in the molten metal to form sulfide CaS with a high melting point. Since CaS has a higher melting point than MnS, it maintains a spherical shape without expanding in the rolling direction during hot working of the wire, and works favorably for improving workability of the wire. Such an effect becomes remarkable at a content of 0.001% or more. On the other hand, if the content exceeds 0.010%, the arc will be disturbed during welding, making stable welding difficult. Therefore, when it is contained, Ca is preferably 0.010% or less. More preferably, it is 0.001% or more and 0.008% or less. More preferably, it is 0.003% or more and 0.006% or less.
  • REM 0.020% or less
  • REM refers to rare earth elements such as Sc, Y, La and Ce. It is a strong deoxidizer and exists in the form of REM oxides in the weld metal.
  • the REM oxide serves as a nucleation site during solidification, thereby refining crystal grains and contributing to an improvement in the strength of the weld metal. Such an effect becomes remarkable at a content of 0.001% or more. However, if the content exceeds 0.020%, arc stability is lowered. Therefore, when it is contained, the REM is preferably 0.020% or less. More preferably, it is 0.001% or more. More preferably, it is 0.005% or more and 0.015% or less.
  • the remaining composition other than the composition described above consists of Fe and unavoidable impurities.
  • unavoidable impurities include O (oxygen), B, Al, Sn, Sb, As, Pb, and Bi.
  • O (oxygen) in the wire is 0.15% or less
  • the amount of B is 0.001% or less
  • the amount of Al is 0.100% or less
  • the amounts of Sn, Sb and As are respectively It is preferable to set the Pb amount and the Bi amount to 0.0001% or less, respectively.
  • the inclusion of unavoidable impurity elements other than these is not prohibited, and such embodiments are also included in the technical scope of the present invention.
  • the solid wire of the present invention is produced by a casting process in which molten steel having the composition described above is melted in a commonly used smelting furnace such as an electric furnace or a vacuum melting furnace and cast into a mold having a predetermined shape, and the resulting steel
  • a heating step of heating an ingot to a predetermined temperature and a hot rolling step of subjecting the heated steel ingot to hot rolling to obtain a steel material (bar-shaped) having a predetermined shape are sequentially performed.
  • the obtained steel material (bar shape) is subjected to multiple cold rolling (cold wire drawing) and, if necessary, an annealing process at an annealing temperature of 900 to 1200° C. to form a wire of desired dimensions. It is preferable to carry out a cold rolling process.
  • the flux cored wire of the present invention has a composition of, for example, 0.05 to 0.20% C-0.15 to 0.30% Si-0.2 to 1.2% Mn-balance Fe.
  • a thin steel plate (thickness 0.5 mm) is used as a steel skin material, and cold-bent in the width direction to form a U shape. Then, metal powder and flux powder for wire whose components are adjusted so as to have a target wire composition are enclosed in the obtained steel outer sheath, and cold drawing is performed to obtain a flux cored wire for SAW. preferably.
  • the metal powder described above is a metal powder or alloy powder having a chemical composition including metal components supplemented to form the welding wire composition of the present invention in total with the chemical composition of the steel outer covering material.
  • the component of the wire flux powder is preferably a flux powder having components equivalent to or similar to those of the welding flux described later.
  • the flux suitable for the welding wire having the composition described above was investigated.
  • the present inventors decided that the flux composition should be a calcia-magnesia basic oxide system, and the basicity [BL] should be a highly basic flux of 1.5 to 2.4. It was found that it is effective to design
  • the basicity [BL] of the flux is an index that indicates the reactivity of the flux, is expressed by the ratio of the basic component to the acidic component of the flux, and is obtained from the following formula (1).
  • the amount of each component in Formula (1) is the amount of components by mass % display.
  • BL (%CaO+%MgO+%BaO+%SrO+% Na2O +% K2O +% Li2O +% CaF2 +0.5%MnO+0.5%FeO)/(% SiO2 +0.5% Al2O3 + 0 .5% TiO 2 +0.5% ZrO 2 ) (1) If the basicity [BL] is less than 1.5, the amount of oxygen in the weld metal increases and the low-temperature toughness is insufficient. , 1.5 to 2.4. Preferably, it is 1.8 or more and 2.2 or less.
  • molten type, sintered type and bond type flux there are molten type, sintered type and bond type flux, but any type can be used.
  • Usable component compositions include calcia-magnesia-based flux in addition to the above-mentioned calcia-magnesia basic oxide flux. From among these, it is necessary to adjust the various oxide components to be blended and adopt a flux having a basicity [BL] of 1.5 to 2.4.
  • Groove processing is performed so that the steel materials to be welded form a predetermined groove shape.
  • the shape of the groove to be formed is not particularly limited, and typical V grooves, double grooves, X grooves, K grooves, etc. for welded steel structures can be exemplified.
  • submerged arc welding may be applied in one pass, but when the welding heat input is controlled or when the plate thickness is large, multilayer welding with two or more passes is applied. ing.
  • multi-layer welding can be appropriately performed in order to increase the strength of the weld metal, and it is preferable to weld three or more layers.
  • the steel used as the base material is particularly intended to be a high Mn-containing steel.
  • the steel materials obtained through the conventional steelmaking process and casting process are hot-rolled by adjusting the heating conditions and rolling reduction, and then cooled to produce steel materials (steel sheets). There are other ways to get it.
  • the thickness of the steel sheet after rolling is, for example, 6 to 100 mm.
  • the high Mn content steel material is a high strength steel material for cryogenic use, and preferably has a Mn content of 15.0 to 30.0%. Specifically, C: 0.20 to 0.80%, Si: 0.15 to 0.90%, Mn: 15.0 to 30.0%, P: 0.030% or less, S: 0.03%. 030% or less, Ni: 3.00% or less, Cr: 1.0 to 8.0%, the balance being Fe and unavoidable impurities.
  • V 2.00% or less
  • Ti 1.00% or less
  • Nb 1.00% or less
  • Al 0.100% or less
  • Cu One or two selected from 1.00% or less
  • N 0.120% or less
  • O (oxygen) 0.0050% or less
  • B 0.0030% or less
  • REM 0.0200% or less It can contain more than one species.
  • C is an inexpensive and important element that has the effect of stabilizing the austenite phase. In order to obtain such an effect, the content of 0.20% or more is required. On the other hand, when the Cr content exceeds 0.80%, Cr carbides are excessively formed and the cryogenic impact toughness is lowered. Therefore, C is preferably in the range of 0.20-0.80%. It is more preferably 0.30% or more and 0.70% or less, and still more preferably 0.40% or more and 0.60% or less.
  • Si 0.15 to 0.90%
  • Si is an element that acts as a deoxidizing agent and contributes to increasing the strength of the steel material by dissolving in steel and solid-solution strengthening. In order to obtain such an effect, the content of 0.15% or more is required. On the other hand, when the content exceeds 0.90%, welding workability is lowered. Therefore, Si is preferably in the range of 0.15 to 0.90%. It is more preferably 0.20% or more and 0.75% or less, and still more preferably 0.30% or more and 0.60% or less.
  • Mn is a relatively inexpensive element that has the effect of stabilizing the austenite phase, and is an important element in the present invention for achieving both high strength and excellent cryogenic toughness. In order to obtain such an effect, the content of 15.0% or more is required. On the other hand, even if the content exceeds 30.0%, the effect of improving the cryogenic toughness is saturated, and the effect commensurate with the content cannot be expected, which is economically disadvantageous. On the other hand, when the content exceeds 30.0% and is large, welding workability and cuttability are lowered, segregation is promoted, and stress corrosion cracking is promoted. Therefore, Mn is preferably in the range of 15.0 to 30.0%. More preferably, it is 17.5% or more and 28.0% or less, and still more preferably 20.0% or more and 26.0% or less.
  • P as an impurity, is an element that segregates at grain boundaries and becomes a starting point for stress corrosion cracking. Therefore, P is preferably in the range of 0.030% or less. More preferably, it is 0.028% or less, and still more preferably 0.024% or less. On the other hand, in order to extremely reduce P to less than 0.002%, refining is required for a long time, and refining costs rise. Therefore, from an economical point of view, P is preferably 0.002% or more.
  • S exists as sulfide-based inclusions in steel and lowers the ductility and cryogenic toughness of steel materials and weld metals. Therefore, it is preferable to reduce S as much as possible, but 0.030% or less is permissible. More preferably, it is 0.010% or less.
  • S is preferably 0.0005% or more.
  • Ni is an element that strengthens austenite grain boundaries, segregates at the grain boundaries, and improves cryogenic impact toughness. In order to obtain such an effect, the content of 0.01% or more is required. In addition, Ni also has the effect of stabilizing the austenite phase, so if the content is further increased, the austenite phase is stabilized and the cryogenic impact toughness of the weld metal is improved. However, Ni is an expensive element, and a content exceeding 3.00% is economically disadvantageous. Therefore, Ni is preferably 0.01% or more and 3.00% or less. More preferably, it is 1.00% or more and 2.00% or less.
  • Cr 1.0 to 8.0%
  • Cr is an element that stabilizes the austenitic phase at cryogenic temperatures and effectively contributes to improving cryogenic toughness and steel strength. Also, it is an effective element for forming a fine crystal region. In order to obtain such effects, it is necessary to contain 1.0% or more of Cr. On the other hand, when the Cr content exceeds 8.0%, Cr carbides are formed, and cryogenic toughness and stress corrosion cracking resistance are lowered. Therefore, Cr is preferably in the range of 1.0 to 8.0%. It is more preferably 2.5% or more and 7.0% or less, and still more preferably 3.5% or more and 6.5% or less.
  • the above-described components are the basic composition of the steel material.
  • optional components include V: 2.00% or less, Ti: 1.00% or less, Nb: 1.00% or less, and Al: 0%. .100% or less, Cu: 1.00% or less, N: 0.120% or less, O (oxygen): 0.0050% or less, B: 0.0030% or less, and REM: 0.0200% or less
  • the steel material composition may contain one or two selected types.
  • V is an element that contributes to the stabilization of the austenite phase and also to the improvement of strength and cryogenic toughness of steel materials.
  • the V content is preferably 0.001% or more.
  • V is preferably 2.00% or less. More preferably, it is 0.003% or more and 1.70% or less. More preferably, it is 1.50% or less.
  • Ti 1.00% or less
  • the carbide becomes coarse and not only becomes a starting point of fracture, but also the coarsening of crystal grains is suppressed and the cryogenic toughness is lowered. It is preferably contained. More preferably, it is 0.50% or less. More preferably, it is 0.30% or less.
  • Nb 1.00% or less
  • the carbide becomes coarse, and not only does it become a starting point of fracture generation, but also the coarsening of crystal grains is suppressed, and the cryogenic toughness decreases. It is preferably contained. More preferably, it is 0.50% or less. More preferably, it is 0.30% or less.
  • Al acts as a deoxidizing agent and is the most commonly used element in the molten steel deoxidizing process for steel materials. In order to obtain such effects, it is preferable to contain 0.001% or more. On the other hand, if the Al content exceeds 0.100%, Al will be mixed into the weld metal portion during welding, resulting in a decrease in the toughness of the weld metal. Therefore, Al is preferably in the range of 0.100% or less. More preferably, it is 0.020% or more and 0.060% or less. More preferably, it is 0.030% or more and 0.040% or less.
  • Cu is an element that contributes to increasing the strength of steel materials through increasing hardenability and solid-solution strengthening. In order to secure such an effect, it is preferable to contain 0.001% or more. On the other hand, if the content exceeds 1.00%, the weldability deteriorates, and defects are likely to occur during steel material production. Therefore, when Cu is contained, the range of Cu is preferably 0.001 to 1.00%. More preferably, it is 0.10% or more and 0.70% or less. More preferably, it is 0.25% or more and 0.60% or less.
  • N is an element that has the effect of stabilizing the austenite phase and effectively contributes to the improvement of cryogenic toughness.
  • the N content is preferably 0.005% or more.
  • N is preferably in the range of 0.005 to 0.120%. More preferably, it is 0.006% or more and 0.040% or less. More preferably, it is 0.020% or more.
  • O (oxygen) exists as oxide-based inclusions in steel and reduces the cryogenic toughness of the steel material. Therefore, it is preferable to reduce O (oxygen) as much as possible, but 0.0050% or less is permissible. Therefore, O (oxygen) is preferably in the range of 0.0050% or less. More preferably, it is 0.0045% or less. On the other hand, in order to extremely reduce O (oxygen) to less than 0.0005%, refining is required for a long time, and the refining cost rises. Therefore, from the viewpoint of economy, O (oxygen) is preferably 0.0005% or more. More preferably, it is 0.0010% or more and 0.0040% or less.
  • B is an element that segregates at grain boundaries and contributes to improving the toughness of steel materials.
  • the B content is preferably 0.0005% or more.
  • B when it is contained, it is preferable that B be in the range of 0.0005 to 0.0030%. More preferably, it is 0.0015% or less. More preferably, it is 0.0010% or less.
  • REM 0.0200% or less
  • REM is an element that has the effect of improving toughness, ductility, and sulfide stress corrosion cracking resistance of steel materials through morphology control of inclusions.
  • REM preferably contains 0.0010% or more in order to obtain the above effects.
  • REM is preferably in the range of 0.0010 to 0.0200%. More preferably, it is 0.0015% or more and 0.015% or less. More preferably, it is 0.0050% or more and 0.010% or less.
  • the balance other than the above components consists of Fe and unavoidable impurities.
  • Ca, Mg, Mo, etc. can be exemplified as the unavoidable impurities, and a total content of 0.05% or less is permissible.
  • the solid wire shown in Table 1 was obtained by melting molten steel having a wire composition in a vacuum melting furnace and casting it into a steel ingot of 1000 kg. The obtained steel ingot was heated to 1200° C., hot rolled, and then cold rolled to prepare a wire for submerged arc welding with a diameter of 4.0 mm.
  • the flux cored wire was prepared by adjusting the metal powder and flux components so as to have the wire composition shown in Table 1.
  • As the outer skin a thin steel sheet having a composition of 0.1% C-0.2% Si-0.5% Mn-balance Fe in mass % was used. The metal powder and the flux whose components were adjusted were enclosed in the above-described outer sheath and drawn to a diameter of 4.0 mm.
  • the components shown in Table 1 are the total values of the shell, metal powder and flux.
  • Welding was carried out using a welding wire (diameter 4.0 mm) with the composition shown in Table 1 and high Mn steel materials for cryogenic use with various compositions shown in Table 2, without preheating, in a downward position, current: 500 to 700 A (AC ), voltage: 30 to 33 V, welding speed: 140 to 300 mm/min, interpass temperature: 100 to 150° C., and 2 to 5 layers.
  • Welding fluxes used were commercially available molten fluxes and bonded fluxes with different basicities of 0.5 to 2.8.
  • the obtained weld metal was evaluated for bead appearance and slag releasability, as well as tensile and impact tests.
  • the tensile test was performed at room temperature for each of three pieces, and the average value of the obtained values (0.2% yield strength) was taken as the tensile property of the weld metal using the wire.
  • the Charpy impact test was performed three times each, and the absorbed energy (vE ⁇ 196 ) at the test temperature of ⁇ 196° C. was determined, and the average value was taken as the cryogenic impact toughness of the weld metal using the wire.
  • the V-notch position of the Charpy impact test piece was set at the center of the weld metal with a plate thickness of 1/2t.
  • Table 3 shows the above results.
  • the asterisk (*) on the upper right of the value of absorbed energy (vE ⁇ 196 ) means the value obtained by performing the Charpy impact test with a 7.5 mm subsize test piece. If the absorbed energy (vE ⁇ 196 ) of the 7.5 mm subsize specimen multiplied by 6/5 is less than the desired absorbed energy (vE ⁇ 196 ) of 28 J for the full size specimen, then the desired cryogenic toughness is It has not been obtained.
  • All of the present invention examples have a yield strength (0.2% yield strength) at room temperature of 400 MPa or more, and a test temperature: -196 ° C. Charpy impact test absorbed energy (vE -196 ) of 28 J or more, high strength and excellent cryogenic toughness. Moreover, in the inventive examples, the slag releasability was good, and a bead with a good shape in which the difference between the maximum value and the minimum value of the bead width was 3 mm or less was obtained.
  • the weld bead shape was poor or the absorbed energy (vE ⁇ 196 ) was less than 28 J.
  • a weld metal having low temperature toughness was not obtained.
  • the basicity of the flux is outside the scope of the present invention, so the oxygen content in the weld metal is high, and the absorbed energy (vE -196 ) at -196°C is desired to be less than 27J.
  • the cryogenic toughness of the steel cannot be ensured.
  • the flux basicity was higher than the range of the present invention, strong slag was formed on the bead surface, the slag removability was poor, and a good bead appearance was not obtained.
  • the content of C and Si in the steel material is lower than the preferred range of the present invention, and the predetermined tensile strength and yield strength are not obtained.
  • the wire had a low Mn content, so the austenite was unstable and the desired impact properties were not obtained.
  • FIG. 1 shows the relationship between the groove cross-sectional area and the welding heat input based on the results of Table 3.
  • FIG. 1 summarizes the welding conditions performed in this test by welding heat input and groove cross-sectional area.
  • the yield strength (0.2% yield strength) at normal temperature exceeded 400 MPa, it was evaluated as " ⁇ ", and the others were evaluated as "X”.
  • the upper side of the straight line in the figure represents the range of the present invention in which the value of groove cross-sectional area [S]/welding heat input [Q] is 0.028 or more. All of the metals exhibit a good yield strength of 400 MPa or more.
  • the welding heat input to each plate thickness and groove is too large, the crystal grains become excessive, and the yield strength is less than 400 MPa, and the required yield I didn't get the strength.

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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2017502842A (ja) * 2013-12-06 2017-01-26 ポスコＰｏｓｃｏ 極低温衝撃靭性に優れた高強度溶接継手部及びこのためのフラックスコアードアーク溶接用ワイヤ
JP6621572B1 (ja) 2018-08-23 2019-12-18 Ｊｆｅスチール株式会社 ガスメタルアーク溶接用ソリッドワイヤ
WO2020203335A1 (ja) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 極低温用高強度溶接継手の製造方法
WO2021075777A1 (ko) * 2019-10-16 2021-04-22 주식회사 포스코 용접봉용 선재 및 이의 제조방법

Family Cites Families (5)

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Publication number Priority date Publication date Assignee Title
JP3152473B2 (ja) * 1992-01-20 2001-04-03 新日本製鐵株式会社 高Ｍｎ非磁性鋼の潜弧溶接方法
CN107052618B (zh) * 2017-03-28 2019-03-19 武汉科技大学 制备lng贮罐的高锰钢用全自动埋弧焊实芯焊丝
CN109623198B (zh) * 2019-01-03 2020-12-18 南京钢铁股份有限公司 一种用于高锰低温钢埋弧焊接的焊丝及焊接方法
CN109530881B (zh) * 2019-01-08 2021-07-09 四川大西洋焊接材料股份有限公司 焊接超低温高锰钢用的埋弧焊焊剂、焊丝及制备方法
CN112846464A (zh) * 2021-01-04 2021-05-28 南京钢铁股份有限公司 一种低温用高锰奥氏体钢埋弧焊接方法

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2017502842A (ja) * 2013-12-06 2017-01-26 ポスコＰｏｓｃｏ 極低温衝撃靭性に優れた高強度溶接継手部及びこのためのフラックスコアードアーク溶接用ワイヤ
JP6621572B1 (ja) 2018-08-23 2019-12-18 Ｊｆｅスチール株式会社 ガスメタルアーク溶接用ソリッドワイヤ
WO2020203335A1 (ja) * 2019-03-29 2020-10-08 Ｊｆｅスチール株式会社 極低温用高強度溶接継手の製造方法
WO2021075777A1 (ko) * 2019-10-16 2021-04-22 주식회사 포스코 용접봉용 선재 및 이의 제조방법

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
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