WO2022030200A1 - ガスメタルアーク溶接用ソリッドワイヤ - Google Patents
ガスメタルアーク溶接用ソリッドワイヤ Download PDFInfo
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- WO2022030200A1 WO2022030200A1 PCT/JP2021/026319 JP2021026319W WO2022030200A1 WO 2022030200 A1 WO2022030200 A1 WO 2022030200A1 JP 2021026319 W JP2021026319 W JP 2021026319W WO 2022030200 A1 WO2022030200 A1 WO 2022030200A1
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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
- B23K9/0026—Arc welding or cutting specially adapted for particular articles or work
-
- 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
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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
- B23K35/3073—Fe as the principal constituent with Mn as next major 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
- B23K35/38—Selection of media, e.g. special atmospheres for surrounding the working area
- B23K35/383—Selection of media, e.g. special atmospheres for surrounding the working area mainly containing noble gases or nitrogen
-
- 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
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- 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
- B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
-
- 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
- B23K9/24—Features related to electrodes
- B23K9/28—Supporting devices for electrodes
- B23K9/29—Supporting devices adapted for making use of shielding means
- B23K9/291—Supporting devices adapted for making use of shielding means the shielding means being a gas
- B23K9/295—Supporting devices adapted for making use of shielding means the shielding means being a gas using consumable electrode-wire
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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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
-
- 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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/18—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
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/04—Tubular or hollow articles
- B23K2101/12—Vessels
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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
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel alloys
-
- 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
- B23K2103/05—Stainless steel
Definitions
- the present invention relates to a solid wire for gas metal arc welding, and more particularly to a solid wire for welding high Mn-containing steel materials used in an extremely low temperature environment.
- liquefied natural gas (hereinafter also referred to as LNG) does not contain sulfur, it is said to be a clean fuel that does not generate air pollutants such as sulfide oxides, and its demand is increasing.
- the container (tank) for transporting or storing LNG is required to maintain excellent ultra-low temperature impact toughness at a temperature of -162 ° C or lower, which is the liquefaction temperature of LNG. ..
- high Mn-containing steel containing about 10 to 35% of Mn in mass% (hereinafter, also referred to as high Mn steel). Is being considered for application.
- the high Mn steel has a characteristic that it is an austenitic phase even at an extremely low temperature, does not cause brittle fracture, and has high strength as compared with austenitic stainless steel. Therefore, there has been a demand for the development of a welding material capable of stably welding such a high Mn-containing steel material.
- Patent Document 1 proposes "a high-strength welded joint portion having excellent ultra-low temperature impact toughness and a flux cored arc welding wire for this purpose".
- the flux cored arc welding wire described in Patent Document 1 has a weight% of C: 0.15 to 0.8%, Si: 0.2 to 1.2%, Mn: 15 to 34%, Cr: 6% or less, Mo: 1.5.
- the Charpy impact test at a test temperature of -196 ° C has excellent low temperature toughness with an absorption energy of 28 J or more and a room temperature tensile strength of 400 MPa or more. It is said that a welded joint with high strength can be effectively obtained, and the wire composition is adjusted to Mo: 1.5% or more, so that a welded joint with excellent high temperature crack resistance can be secured.
- Patent Document 1 has a problem that the amount of fume generated during welding increases and the welder is exposed to an environment with a large amount of fume.
- the present invention solves the above-mentioned problems of the prior art, has a small amount of toughness during welding, and has high strength and excellent ultra-low temperature, which is suitable as a welding material for high Mn-containing steel materials used in an extremely low temperature environment. It is an object of the present invention to provide a solid wire for gas metal arc welding capable of producing a welded joint portion having both toughness.
- “high strength” here means that 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, and “excellent pole”.
- “Low temperature toughness” means the case where the absorbed energy vE -196 of the Charpy impact test at the test temperature: -196 ° C of the weld metal manufactured in accordance with JIS Z 3111 is 28J or more.
- the present inventors first diligently examined the factors affecting the amount of fume generated during gas metal arc welding. As a result, in order to significantly reduce the amount of fume generated, it was found that it is effective to use a solid wire as the welding material instead of the flux cored wire.
- a solid wire having a larger amount of processing during wire drawing than a flux cored wire is liable to crack or break during wire drawing, especially when the wire composition has a high Mn content, and the solid wire. There was a problem that the manufacturability of the wire was lowered.
- the present inventors have diligently studied various factors affecting the manufacturability of the wire. As a result of investigating the fracture surface where cracks and disconnections occurred, it was found that the starting point was coarse Al 2 O 3 of 10 ⁇ m or more. Therefore, it was found that by suppressing the formation of coarse Al 2 O 3 , wire drawing can be performed without the occurrence of defects such as cracks. In order to suppress the formation of coarse Al 2 O 3 , it is important to adjust the wire composition so that Al is 0.020% or less and O (oxygen) is 0.010% or less in mass%. I found that there is.
- the solid wire composition required to obtain a welded metal having the desired excellent ultra-low temperature toughness was investigated. As a result, the solid wire was adjusted in the range of C: 0.20 to 0.80%, Si: 0.15 to 0.90% by mass%, and further Mn: 15.0 to 30.0%, Ni: 0.01 to 10.00%, Cr: 6.0 to 15.0.
- the present invention has been completed with further studies based on such findings.
- 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: 15.0 to 30.0%, P: 0.030% or less, S: 0.030% or less, Al: 0.020% or less, Ni: 0.01-10.00%, Cr: 6.0-15.0%, Mo: 0.01-3.50%, O: 0.010% or less, N: Solid wire for gas metal arc welding containing 0.120% or less and having a composition consisting of the balance Fe and unavoidable impurities.
- High Mn-containing steel containing 10 to 35% of Mn, By 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, Al: 0.020% or less, Ni: 0.01-10.00%, Cr: 6.0-15.0%, Mo: 0.01-3.50%, O: 0.010% or less, N: Using a solid wire for gas metal arc welding containing 0.120% or less and having a composition consisting of the balance Fe and unavoidable impurities.
- a mixed gas of 10-40% CO 2 gas and an inert gas consisting of the balance Ar is used as a shield gas, the welding current is 180-330A, and the amount of fume generated is 1200mg / min.
- Test temperature Charpy impact test at -196 ° C Forming welded joints with excellent low-temperature toughness with absorption energy of 28 J or more and high strength with normal temperature tensile strength of 400 MPa or more
- Test temperature Charpy impact test at -196 ° C Forming welded joints with excellent low-temperature toughness with absorption energy of 28 J or more and high strength with normal temperature tensile strength of 400 MPa or more
- the gas metal arc welding method according to any one.
- the wire manufacturability is excellent, the amount of fume generated during gas metal arc welding can be remarkably suppressed, and the welded joint portion having high strength and excellent ultra-low temperature toughness as a welding material for high Mn-containing steel materials. It is possible to provide a solid wire for gas metal arc welding that can be easily manufactured, and it is extremely effective in industry.
- the present invention is a solid wire for gas metal arc welding suitable for gas metal arc welding of steel materials containing high Mn.
- the weld metal produced by gas metal arc welding in accordance with JIS Z3111 has a high strength of 400 MPa or more with a 0.2% toughness at room temperature and a Charpy impact test at a test temperature of -196 ° C. It is a welded metal that has excellent ultra-low temperature toughness with an absorption energy of 28 J or more, and is a welding material capable of producing a welded joint portion having high strength and excellent ultra-low temperature toughness.
- the solid wire of the present invention has a basic composition of 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, Al: It contains 0.020% or less, Ni: 0.01 to 10.00%, Cr: 6.0 to 15.0%, Mo: 0.01 to 3.50%, O: 0.010% or less, N: 0.120% or less, and has a composition consisting of the balance Fe and unavoidable impurities. ..
- C 0.20-0.80% C is an element having an action of increasing the strength of the weld metal by strengthening the solid solution, and C stabilizes the austenite phase and improves the ultra-low temperature impact toughness of the weld metal. In order to obtain such an effect, a content of 0.20% or more is required. However, if it is contained in excess of 0.80%, carbides are precipitated, the cryogenic toughness is lowered, and high temperature cracking at the time of welding is likely to occur. Therefore, C was limited to the range of 0.20 to 0.80%.
- the content of C is preferably 0.40% or more.
- the content of C is preferably 0.60% or less.
- Si acts as a deoxidizing agent, has the effect of increasing the yield of Mn, increasing the viscosity of the molten metal, stably maintaining the bead shape, and reducing the occurrence of spatter. In order to obtain such an effect, a content of 0.15% or more is required. However, if it is contained in excess of 0.90%, the cryogenic toughness of the weld metal is reduced. Further, Si segregates during solidification and forms a liquid phase at the interface of the solidified cell, which lowers the high temperature crack resistance. Therefore, Si was limited to the range of 0.15 to 0.90%. Preferably, Si is 0.20% or more. Preferably, Si is 0.70% or less.
- Mn 15.0-30.0%
- Mn is an element that stabilizes the austenite phase at low cost, and the content of Mn is required to be 15.0% or more in the present invention. If Mn is less than 15.0%, a ferrite phase is formed in the weld metal and the toughness at extremely low temperatures is significantly reduced. On the other hand, when Mn exceeds 30.0%, excessive Mn segregation occurs during solidification, inducing high-temperature cracking. Therefore, Mn was limited to the range of 15.0 to 30.0%. Preferably, Mn is 18.0% or more. Preferably, Mn is 27.0% or less.
- P 0.030% or less
- P is an element that segregates at grain boundaries and induces high-temperature cracking. In the present invention, it is preferable to reduce it as much as possible, but 0.030% or less is acceptable. Therefore, P was limited to 0.030% or less. Excessive reduction leads to an increase in refining cost. Therefore, it is preferable to adjust P to 0.003% or more.
- S 0.030% or less S exists as a sulfide-based inclusion MnS in the weld metal. Since MnS is the starting point of fracture, it reduces cryogenic toughness. Therefore, S was limited to 0.030% or less. Excessive reduction leads to an increase in refining cost. Therefore, it is preferable to adjust S to 0.001% or more.
- Al 0.020% or less
- Al is an element that acts as a deoxidizing agent and is added when steel is melted. When Al is added in excess of 0.020%, coarse Al 2 O 3 is formed, which becomes the starting point of fracture during wire drawing and disconnection occurs. Therefore, Al was limited to 0.020% or less. It should be noted that it is preferably 0.015% or less, more preferably less than 0.009%.
- Ni 0.01-10.00%
- Ni is an element that reinforces austenite grain boundaries and segregates at grain boundaries to improve cryogenic 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 toughness of the weld metal is improved.
- Ni is an expensive element, and a content of more than 10.00% is economically disadvantageous. Therefore, Ni was limited to 0.01 to 10.00%.
- Ni is preferably 0.20% or more.
- Ni is preferably 8.00% or less.
- Cr acts as an element that stabilizes the austenite phase at cryogenic temperatures, improving the cryogenic toughness of the weld metal. Cr also has the effect of improving the strength of the weld metal. Further, Cr works effectively to increase the liquidus line of the molten metal and suppress the occurrence of high temperature cracking. Further, Cr also has an effect of suppressing high temperature cracking due to P by forming CrP in the liquid phase. In order to obtain such an effect, the content of 6.0% or more is required. If Cr is less than 6.0%, the above effect cannot be ensured. On the other hand, if it is contained in excess of 15.0%, Cr carbide is generated, which causes a decrease in cryogenic toughness. Furthermore, due to the formation of carbides, the workability at the time of wire drawing is lowered. Therefore, Cr was limited to the range of 6.0 to 15.0%. Preferably, Cr is 7.0% or more.
- Mo 0.01% to 3.50%
- Mo is an element that reinforces austenite grain boundaries and segregates at the grain boundaries to improve the strength of the weld metal. Such an effect becomes remarkable when the content is 0.01% or more. If the content exceeds 0.01%, it also has the effect of improving the strength of the weld metal by strengthening the solid solution. On the other hand, if it is contained in an amount of more than 3.50%, it precipitates as a carbide and the hot workability is lowered, and cracks are induced when the wire is drawn, so that the manufacturability of the wire is lowered. Therefore, Mo was limited to the range of 0.01 to 3.50%. Mo is preferably 0.1% or more. Preferably, Mo is 3.0% or less.
- O 0.010% or less
- O (oxygen) is an element that is inevitably mixed, and a deoxidizing agent such as Al, Si, or Mn is added to float and separate it as an oxide.
- a coarse oxide is formed, and especially when Al is added in an amount of more than 0.020%, a coarse Al 2 O 3 (oxide) is formed.
- These coarse oxides (Al 2 O 3 ) serve as the starting point of fracture, which reduces the manufacturability of the wire. Therefore, O (oxygen) was limited to 0.010% or less.
- O (oxygen) is preferably 0.008% or less.
- N 0.120% or less
- N is an element that is inevitably mixed, but like C, it effectively contributes to improving the strength of the weld metal, stabilizes the austenite phase, and contributes to the stable improvement of ultra-low temperature toughness. do. Such an effect becomes remarkable when N is contained in an amount of 0.003% or more.
- N when N is contained in an amount of more than 0.120%, a nitride is formed and the low temperature toughness is lowered. Therefore, N was limited to 0.120% or less.
- N is 0.004% or more.
- N is 0.080% or less.
- the above-mentioned components are the basic components, but in the present invention, in addition to the above-mentioned basic composition, if necessary as a selection component, V: 1.0% or less, Ti: 1.0%.
- V 1.0% or less
- Ti 1.0%.
- Nb 1.0% or less
- Ca 0.010% or less
- REM 0.020% or less. Two or more types can be selected and contained.
- the solid wire of the present invention can contain one or more selected types, if necessary.
- V is a carbide-forming element, which precipitates fine carbides and contributes to improving the strength of the weld metal.
- V is contained in an amount of 0.001% or more, but if V is contained in an amount of more than 1.0%, the carbide becomes coarse and the starting point of cracking during wire drawing of the solid wire. Therefore, the wire drawing workability is lowered and the wire manufacturability is lowered. Therefore, when it is contained, it is preferable to limit V to 1.0% or less.
- V is 0.002% or more.
- V is preferably 0.8% or less.
- Ti is a carbide-forming element, which precipitates fine carbides and contributes to improving the strength of the weld metal. Further, Ti deposits carbides on the interface of the solidified cell of the weld metal and contributes to suppressing the occurrence of high temperature cracking. In order to obtain such an effect, it is desirable to contain Ti of 0.001% or more, but if Ti is contained in excess of 1.0%, carbides become coarse and cracks occur during wire drawing of solid wire. It serves as a starting point, lowers wire drawing workability, and lowers wire manufacturability. Therefore, when Ti is contained, it is preferable to limit Ti to 1.0% or less. Ti is preferably 0.002% or more. Ti is preferably 0.8% or less.
- Nb is a carbide-forming element, which is an element that precipitates carbides and contributes to improving the strength of the weld metal.
- Nb precipitates carbides at the interface of the solidified cell of the weld metal, which contributes to suppressing the occurrence of high-temperature cracking.
- Nb it is desirable to contain 0.001% or more, but if Nb exceeds 1.0%, the carbides become coarse and become the starting point of cracking during wire drawing of solid wire, and the wire is drawn. It reduces workability and reduces wire manufacturability. Therefore, when Nb is contained, it is preferable to limit Nb to 1.0% or less.
- Nb is 0.002% or more.
- Nb is 0.8% or less.
- Cu 1.00% or less, Ca: 0.010% or less and REM: 0.020% or less
- Cu is an element that contributes to austenite stabilization, and Ca and REM contribute to improving workability. It is an element to be used, and can be selected as necessary and contains one kind or two or more kinds.
- Cu is an element that stabilizes the austenite phase, stabilizes the austenite phase even at extremely low temperatures, and improves the cryogenic toughness of the weld metal. In order to obtain such an effect, it is desirable that Cu is contained in an amount of 0.01% or more. However, if Cu is contained in a large amount exceeding 1.00%, the hot ductility is lowered and the manufacturability of the wire is lowered. Therefore, when it is contained, it is preferable to limit Cu to 1.00% or less. More preferably, Cu is 0.02% or more. Preferably, Cu is 0.8% or less.
- Ca combines with S in the molten metal to form a high melting point sulfide CaS. Since CaS has a higher melting point than MnS, it maintains a spherical shape without advancing in the rolling direction during hot working of solid wire, which is advantageous for improving workability of solid wire. Such an effect becomes remarkable when the content of Ca is 0.001% or more. On the other hand, if Ca is contained in an amount of more than 0.010%, the arc is disturbed during welding, which makes stable welding difficult. Therefore, when it is contained, it is preferable to limit Ca to 0.010% or less. More preferably, Ca is 0.001% or more. Ca is preferably 0.008% or less.
- REM is a powerful deoxidizer and exists in the form of REM oxide in weld metals.
- the REM oxide becomes a nucleation site during solidification, which makes the crystal grains finer and contributes to the improvement of the strength of the weld metal. Such an effect becomes remarkable when the content is 0.001% or more. However, if it is contained in excess of 0.020%, the stability of the arc will decrease. Therefore, when it is contained, it is preferable to limit the REM to 0.020% or less. More preferably, REM is 0.002% or more. Preferably REM is 0.018% or less.
- the rest other than the above components consist of Fe and unavoidable impurities.
- the method for manufacturing the solid wire of the present invention will be described.
- the production of the solid wire of the present invention does not need to be particularly limited to the production method other than using the molten steel having the above-mentioned composition, and any of the conventional methods for producing a solid wire for welding can be applied.
- the solid wire of the present invention was obtained by a casting step of melting molten steel having the above-mentioned composition in a common rolling mill such as an electric furnace or a vacuum melting furnace and casting it into a mold having a predetermined shape.
- a heating step of heating the ingot to a predetermined temperature and a hot rolling step of hot rolling the heated steel ingot to obtain a steel material (rod shape) having a predetermined shape were sequentially performed, and then obtained.
- the steel material (rod-shaped) is cold-rolled multiple times (cold wire drawing) and, if necessary, annealed to an annealing temperature of 900 to 1200 ° C. to obtain a wire of the desired size. It is preferable to carry out the process.
- the present invention can be implemented as a gas metal arc welding method.
- the gas metal arc welding method according to the present invention comprises high Mn-containing steel containing 10 to 35% of Mn 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, Al: 0.020% or less, Ni: 0.01-10.00%, Cr: 6.0-15.0%, Mo: 0.01-3.50%, O: 0.010% or less
- N Using a solid wire for gas metal arc welding containing 0.120% or less and having a composition consisting of the balance Fe and unavoidable impurities, from 10-40% CO 2 gas and the balance Ar in accordance with JIS Z 3930-2013.
- this gas metal arc welding method can be carried out as a gas metal arc welding method in which a mixed gas with an inert gas is used as a shield gas and gas metal arc welding is performed at a welding current of 180 to 330 A and a fume generation amount of 1200 mg / min or less.
- this gas metal arc welding method is a gas that forms a welded joint with excellent low temperature toughness with a Charpy impact test absorption energy of 28 J or more at a test temperature of -196 ° C and high strength with a normal temperature tensile strength of 400 MPa or more. It can be carried out as a metal arc welding method.
- the above component composition further contains one or more selected from V: 1.0% or less, Ti: 1.0% or less and Nb: 1.0% or less in mass%. You may.
- the above-mentioned component composition may further contain one or more selected from Cu: 1.00% or less, Ca: 0.010% or less, and REM: 0.020% or less in mass%.
- the present invention can also be carried out as a method for manufacturing a welded joint using the above-mentioned gas metal arc welding method.
- the molten steel having the composition shown in Table 1 was melted in a vacuum melting furnace and cast to make 1000 kg of steel ingot.
- the obtained ingot was heated to 1200 ° C., then hot-rolled and then cold-rolled to obtain a 1.2 mm ⁇ solid wire for gas metal arc welding.
- the manufacturability of each solid wire was evaluated by measuring the rolling load (wire drawing load), observing cracks, observing the cross section of the wire, and the like. If it is judged that rolling (wire drawing) processing is impossible due to a high rolling load (wire drawing load), if cracks are found, it is possible to proceed further due to the cracks that have occurred.
- the wire manufacturability was evaluated as "x" when it became impossible. Other than that, the wire manufacturability was evaluated as " ⁇ ".
- a steel outer skin and a flux cored wire in which the metal powder and the flux powder were encapsulated in the steel outer skin were produced.
- a thin steel plate (thickness 0.5 mm) having a composition of 0.1% C-0.2% Si-0.5% Mn-remaining Fe in mass% is used as a steel outer skin material and is cold-bent in the width direction to form a U-shape. The shape was used.
- the obtained steel outer skin is filled with the metal powder and the flux powder whose components have been adjusted so as to have the wire composition shown in Table 2, and the wire is drawn cold to obtain a flux cored wire for welding (diameter). : 1.2mm ⁇ ).
- the components shown in Table 2 are the total values of the steel outer skin, the metal powder and the flux powder.
- gas metal arc welding is performed in a welded fume collector in accordance with the regulations of JIS Z3930, and the generated fume is filtered (glass fiber).
- the amount of fume generated was measured.
- the welding conditions for gas metal arc welding were current: 250A, voltage: 34V, welding speed: 30cm / min, shield gas: 80% Ar + 20% CO 2 (flow rate: 20L / min).
- a high Mn-containing steel plate for ultra-low temperature (plate thickness: 12 mm) was prepared as a test plate, and the solid wire or flux obtained by abutting to form a 45 ° V groove in accordance with JIS Z3111. Gas metal arc welding was performed using the cored wire as a welding material to obtain a weld metal in the groove described above.
- the high Mn-containing steel sheet for cryogenic temperature used as a test plate is a steel sheet having a composition of 0.5% C ⁇ 0.4% Si-25% Mn-3-% Cr—residue Fe in mass%.
- Gas metal arc welding uses solid wires (1.2 mm in diameter) or flux cored wires (1.2 mm in diameter) with the compositions shown in Tables 1 and 2, with no preheating, in a downward position, and current: 180-330 A. (DCEP), voltage: 24-33V, welding speed: 30cm / min, pass interval: 100-150 ° C, shield gas: Ar-10-40% CO 2 .
- weld metal was observed with an optical microscope to determine the presence or absence of welding cracks.
- Weld cracks are high-temperature cracks, and if cracks are observed, they are evaluated as "x" because the high-temperature crack resistance is reduced. When no cracking was observed, it was evaluated as " ⁇ " because of its excellent high temperature cracking resistance.
- the appearance of the weld bead was visually observed to determine the appearance of the weld bead.
- the appearance of the weld bead was evaluated as "x" as poor.
- the bead appearance was evaluated as “ ⁇ ” as good.
- a tensile test piece (parallel part diameter 6 mm ⁇ ) of the weld metal and a Charpy impact test piece (V notch) of the weld metal are collected in accordance with JIS Z3111, and the tensile test and impact are performed. The test was carried out.
- All of the examples of the present invention have excellent wire manufacturability, and the amount of fume generated when gas metal arc welding is performed with a welding current of 250 A in accordance with JIS Z3930-2013 is 1200 mg / min or less, and fume. It can be said that it is a welding material with a small amount of generation.
- all of the examples of the present invention are welding materials that do not generate welding cracks (high temperature cracks) during welding, have excellent high temperature crack resistance, and can obtain a welded metal having a good weld bead appearance.
- the yield strength (0.2% proof stress) at room temperature is 400 MPa or more
- the absorbed energy vE -196 of the Charpy impact test at the test temperature: -196 ° C is 28 J or more, which is high strength and excellent. It can be said that it is a welding material (solid wire) capable of obtaining a weld metal having both ultra-low temperature toughness.
- the amount of fume generated exceeds 1200 mg / min, the wire manufacturability is poor, or welding cracks (high temperature cracks) occur and the high temperature crack resistance is lowered. Whether the weld bead is defective and the appearance of the weld bead is poor, or the 0.2% proof stress at room temperature is less than 400 MPa, or the absorbed energy vE -196 is less than 28 J, at the time of desired welding. Welded metal with a small amount of fume generation and high strength and excellent ultra-low temperature toughness has not been obtained.
- the 0.2% proof stress of the weld metal is less than 400 MPa, which is the desired high strength. Has not been secured. Furthermore, high temperature cracking has occurred in wire No. 15.
- the wire No. 16 which is a comparative example has a high temperature crack because the Mn content is high outside the range of the present invention.
- the wire No. 17 as a comparative example has a Ti and Nb content
- the wire No. 18 has an Al content
- the wire No. 19 has an O (oxygen) content, which are far from the scope of the present invention. Therefore, the wire drawing workability deteriorated, and the wire could not be drawn to a desired wire diameter.
- the wire No. 20 as a comparative example has a low Mn content outside the range of the present invention, so that the stability of the austenite phase is low. Is declining.
- the absorption energy vE -196 is less than 28J, and the cryogenic toughness is lowered.
- the wire No. 22 as a comparative example has a Si content
- the wire No. 23 has a P content
- the wire No. 24 has a C content. Is generated, and the high temperature crack resistance is lowered.
- the absorption energy vE -196 is less than 28 J, and the cryogenic toughness is lowered.
- the wire No. 25 which is a comparative example, since the amount of Si is low outside the range of the present invention, a good bead shape cannot be obtained and pits are generated.
- the wires No. 26, No. 27, No. 28, and No. 29, which are comparative examples, are all flux cored wires, the amount of fumes generated exceeds 1200 mg / min, and a large amount of fumes is generated during welding. is doing.
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Abstract
Description
本発明の要旨は、次のとおりである。
[1] 質量%で、
C:0.20~0.80%、 Si:0.15~0.90%、
Mn:15.0~30.0%、 P:0.030%以下、
S:0.030%以下、 Al:0.020%以下、
Ni:0.01~10.00%、 Cr:6.0~15.0%、
Mo:0.01~3.50%、 O:0.010%以下、
N:0.120%以下
を含み、残部Feおよび不可避的不純物からなる組成を有するガスメタルアーク溶接用ソリッドワイヤ。
[2] 前記組成に加えてさらに、質量%で、V:1.0%以下、Ti:1.0%以下およびNb:1.0%以下のうちから選ばれた1種または2種以上を含有する[1]に記載のガスメタルアーク溶接用ソリッドワイヤ。
[3] 前記組成に加えてさらに、質量%で、Cu:1.00%以下、Ca:0.010%以下およびREM:0.020%以下のうちから選ばれた1種または2種以上を含有する[1]または[2]に記載のガスメタルアーク溶接用ソリッドワイヤ。
[4] Mnを10~35%含有する高Mn含有鋼を、
質量%で、
C:0.20~0.80%、 Si:0.15~0.90%、
Mn:15.0~30.0%、 P:0.030%以下、
S:0.030%以下、 Al:0.020%以下、
Ni:0.01~10.00%、 Cr:6.0~15.0%、
Mo:0.01~3.50%、 O:0.010%以下、
N:0.120%以下
を含み、残部Feおよび不可避的不純物からなる組成を有するガスメタルアーク溶接用ソリッドワイヤを用い、
JIS Z 3930-2013に準拠して、10~40%CO2ガスと残部Arからなる不活性ガスとの混合ガスをシールドガスとして用い、溶接電流: 180~330Aで、ヒューム発生量が1200mg/min以下でガスメタルアーク溶接を行うガスメタルアーク溶接方法。
[5] 前記組成に加えてさらに、質量%で、V:1.0%以下、Ti:1.0%以下およびNb:1.0%以下のうちから選ばれた1種または2種以上を含有する[4]に記載のガスメタルアーク溶接方法。
[6] 前記組成に加えてさらに、質量%で、Cu:1.00%以下、Ca:0.010%以下およびREM:0.020%以下のうちから選ばれた1種または2種以上を含有する[4]または[5]に記載のガスメタルアーク溶接方法。
[7] 試験温度:-196℃におけるシャルピー衝撃試験吸収エネルギーが28J以上の優れた低温靭性および常温引張強さが400MPa以上の高強度を有する溶接継手部を形成する[4]ないし[6]のいずれかに記載のガスメタルアーク溶接方法。
[8] 請求項4ないし7のいずれかに記載のガスメタルアーク溶接方法を用いた溶接接手の製造方法。
Cは、固溶強化により、溶接金属の強度を上昇させる作用を有する元素であり、また、Cは、オーステナイト相を安定化させ、溶接金属の極低温衝撃靭性を向上させる。このような効果を得るためには、0.20%以上の含有を必要とする。しかし、0.80%を超えて含有すると、炭化物が析出し、極低温靭性が低下し、さらに、溶接時の高温割れが生じやすくなる。そのため、Cは0.20~0.80%の範囲に限定した。Cの含有量は、好ましくは、0.40%以上である。Cの含有量は、好ましくは、0.60%以下である。
Siは、脱酸剤として作用し、Mnの歩留りを高めるとともに、溶融金属の粘性を高め、ビード形状を安定的に保持し、スパッタの発生を低減する効果がある。そのような効果を得るためには、0.15%以上の含有を必要とする。しかし、0.90%を超えて含有すると、溶接金属の極低温靭性を低下させる。また、Siは、凝固時に偏析し、凝固セル界面に液相を生成して、耐高温割れ性を低下させる。そのため、Siは0.15~0.90%の範囲に限定した。好ましくは、Siは、0.20%以上である。好ましくは、Siは、0.70%以下である。
Mnは、安価に、オーステナイト相を安定化する元素であり、本発明では15.0%以上の含有を必要とする。Mnが15.0%未満では、溶接金属中にフェライト相が生成し,極低温での靭性が著しく低下する。一方、Mnが30.0%を超えると、凝固時に過度のMn偏析が発生し,高温割れを誘発する。そのため、Mnは15.0~30.0%の範囲に制限した。好ましくは、Mnは、18.0%以上である。好ましくは、Mnは、27.0%以下である。
Pは、結晶粒界に偏析し、高温割れを誘発する元素であり、本発明では、できるだけ低減することが好ましいが、0.030%以下であれば、許容できる。そのため、Pは0.030%以下に限定した。なお、過度の低減は、精練コストの高騰を招く。そのため、Pは0.003%以上に調整することが好ましい。
Sは、溶接金属中では、硫化物系介在物MnSとして存在する。MnSは、破壊の発生起点となるため、極低温靭性を低下させる。そのため、Sは0.030%以下に限定した。なお、過度の低減は、精練コストの高騰を招く。そのため、Sは0.001%以上に調整することが好ましい。
Alは、脱酸剤として作用する元素であり、鋼の溶解時に添加される。Alを0.020%を超えて添加すると粗大なAl2O3が形成され、ワイヤの伸線加工時に破壊の発生起点となり、断線が生じる。そのため、Alは0.020%以下に限定した。なお、好ましくは0.015%以下、より好ましくは0.009%未満である。
Niは、オーステナイト粒界を強化する元素であり、粒界に偏析し、極低温靱性を向上させる。このような効果を得るためには、0.01%以上の含有を必要とする。また、Niは、オーステナイト相を安定化する効果もあるため、さらに含有量を増加すれば、オーステナイト相を安定化させて、溶接金属の極低温靭性を向上させる。しかし、Niは高価な元素であり、10.00%を超える含有は、経済的に不利となる。そのため、Niは0.01~10.00%に限定した。好ましくはNiは0.20%以上である。好ましくはNiは8.00%以下である。
Crは、極低温ではオーステナイト相を安定化させる元素として働き、溶接金属の極低温靭性を向上させる。また、Crは、溶接金属の強度を向上させる作用も有する。また、Crは、溶融金属の液相線を高めて、高温割れの発生を抑制するのに有効に作用する。さらに、Crは、液相中でCrPを形成することで、Pによる高温割れを抑制する作用も有する。このような効果を得るためには6.0%以上の含有を必要とする。Crが6.0%未満では、上記した効果を確保できない。一方、15.0%を超えて含有すると、Cr炭化物が生成し、極低温靭性の低下を招く。またさらに、炭化物の生成により、ワイヤ伸線時の加工性が低下する。そのため、Crは6.0~15.0%の範囲に限定した。好ましくは、Crは7.0%以上である。
Moは、オーステナイト粒界を強化する元素であり、粒界に偏析し、溶接金属の強度を向上させる。このような効果は0.01%以上の含有で顕著となる。なお、0.01%を超える含有では、固溶強化により溶接金属の強度を向上させる作用も有する。一方、3.50%を超えて含有すると、炭化物として析出し、熱間加工性が低下し、また、ワイヤの伸線時に割れを誘発させるなど、ワイヤの製造性が低下する。そのため、Moは0.01~3.50%の範囲に限定した。好ましくはMoは0.1%以上である。好ましくは、Moは3.0%以下である。
O(酸素)は、不可避的に混入する元素であり、AlやSi、Mnなどの脱酸剤を添加し、酸化物として浮上分離される。Oが0.010%を超えると粗大な酸化物を形成し、とくにAlが0.020%を超えて添加される場合には、粗大なAl2O3(酸化物)を形成する。これら粗大な酸化物(Al2O3)が破壊の発生起点となり、ワイヤの製造性が低下する。このため、O(酸素)は0.010%以下に限定した。なお、好ましくはO(酸素)は0.008%以下である。
Nは、不可避的に混入する元素であるが、Cと同様に、溶接金属の強度向上に有効に寄与するとともに、オーステナイト相を安定化し、極低温靱性の安定的向上に寄与する。このような効果は、Nは0.003%以上の含有で顕著となる。一方、Nは0.120%を超えて含有すると、窒化物を形成し、低温靱性が低下する。そのため、Nは0.120%以下に限定した。好ましくはNは0.004%以上である。好ましくは、Nは0.080%以下である。
V、Ti、Nbはいずれも、炭化物の形成を促進し、溶接金属の強度向上に寄与する元素であり、必要に応じて本発明のソリッドワイヤは、選択した1種または2種以上を含有できる。
Cuはオーステナイト安定化に寄与する元素であり、Ca、REMは加工性向上に寄与する元素であり、必要に応じて選択して1種または2種以上を含有できる。
つぎに、本発明のソリッドワイヤの製造方法について説明する。
本発明のソリッドワイヤの製造は、上記した組成を有する溶鋼を使用すること以外、とくにその製造方法を限定する必要はなく、常用の溶接用ソリッドワイヤの製造方法がいずれも適用できる。
また、本発明は、ガスメタルアーク溶接方法として実施することができる。本発明に係るガスメタルアーク溶接方法は、Mnを10~35%含有する高Mn含有鋼を、質量%で、
C:0.20~0.80%、 Si:0.15~0.90%、
Mn:15.0~30.0%、 P:0.030%以下、
S:0.030%以下、 Al:0.020%以下、
Ni:0.01~10.00%、 Cr:6.0~15.0%、
Mo:0.01~3.50%、 O:0.010%以下、
N:0.120%以下
を含み、残部Feおよび不可避的不純物からなる組成を有するガスメタルアーク溶接用ソリッドワイヤを用い、JIS Z 3930-2013に準拠して、10~40%CO2ガスと残部Arからなる不活性ガスとの混合ガスをシールドガスとして用い、溶接電流:180~330Aでヒューム発生量が1200mg/min以下でガスメタルアーク溶接を行うガスメタルアーク溶接方法として実施することができる。
また、このガスメタルアーク溶接方法は、試験温度:-196℃におけるシャルピー衝撃試験吸収エネルギーが28J以上の優れた低温靭性および常温引張強さが400MPa以上の高強度を有する溶接継手部を形成するガスメタルアーク溶接方法として実施することができる。
ガスメタルアーク溶接方法において、上記成分組成は、さらに、質量%で、V:1.0%以下、Ti:1.0%以下およびNb:1.0%以下のうちから選ばれた1種または2種以上を含有してもよい。上記成分組成は、さらに、質量%で、Cu:1.00%以下、Ca:0.010%以下およびREM:0.020%以下のうちから選ばれた1種または2種以上を含有してもよい。
本発明は、上記のガスメタルアーク溶接方法を用いた溶接接手の製造方法としても実施することができる。
Claims (8)
- 質量%で、
C:0.20~0.80%、 Si:0.15~0.90%、
Mn:15.0~30.0%、 P:0.030%以下、
S:0.030%以下、 Al:0.020%以下、
Ni:0.01~10.00%、 Cr:6.0~15.0%、
Mo:0.01~3.50%、 O:0.010%以下、
N:0.120%以下
を含み、残部Feおよび不可避的不純物からなる組成を有するガスメタルアーク溶接用ソリッドワイヤ。 - 前記組成に加えてさらに、質量%で、V:1.0%以下、Ti:1.0%以下およびNb:1.0%以下のうちから選ばれた1種または2種以上を含有する請求項1に記載のガスメタルアーク溶接用ソリッドワイヤ。
- 前記組成に加えてさらに、質量%で、Cu:1.00%以下、Ca:0.010%以下およびREM:0.020%以下のうちから選ばれた1種または2種以上を含有する請求項1または2に記載のガスメタルアーク溶接用ソリッドワイヤ。
- Mnを10~35%含有する高Mn含有鋼を、
質量%で、
C:0.20~0.80%、 Si:0.15~0.90%、
Mn:15.0~30.0%、 P:0.030%以下、
S:0.030%以下、 Al:0.020%以下、
Ni:0.01~10.00%、 Cr:6.0~15.0%、
Mo:0.01~3.50%、 O:0.010%以下、
N:0.120%以下
を含み、残部Feおよび不可避的不純物からなる組成を有するガスメタルアーク溶接用ソリッドワイヤを用い、
JIS Z 3930-2013に準拠して、10~40%CO2ガスと残部Arからなる不活性ガスとの混合ガスをシールドガスとして用い、溶接電流: 180~330Aで、ヒューム発生量が1200mg/min以下でガスメタルアーク溶接を行うガスメタルアーク溶接方法。 - 前記組成に加えてさらに、質量%で、V:1.0%以下、Ti:1.0%以下およびNb:1.0%以下のうちから選ばれた1種または2種以上を含有する請求項4に記載のガスメタルアーク溶接方法。
- 前記組成に加えてさらに、質量%で、Cu:1.00%以下、Ca:0.010%以下およびREM:0.020%以下のうちから選ばれた1種または2種以上を含有する請求項4または5に記載のガスメタルアーク溶接方法。
- 試験温度:-196℃におけるシャルピー衝撃試験吸収エネルギーが28J以上の優れた低温靭性および常温引張強さが400MPa以上の高強度を有する溶接継手部を形成する請求項4ないし6のいずれかに記載のガスメタルアーク溶接方法。
- 請求項4ないし7のいずれかに記載のガスメタルアーク溶接方法を用いた溶接接手の製造方法。
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WO2022186096A1 (ja) * | 2021-03-01 | 2022-09-09 | Jfeスチール株式会社 | サブマージアーク溶接継手 |
CN115125441A (zh) * | 2022-06-16 | 2022-09-30 | 江苏永钢集团有限公司 | 一种气保焊丝用钢及其热处理软化方法 |
JP7494966B1 (ja) | 2023-03-13 | 2024-06-04 | Jfeスチール株式会社 | ガスメタルアーク溶接方法 |
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