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WO2015068261A1 - Procédé pour produire un joint soudé - Google Patents

Procédé pour produire un joint soudé Download PDF

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Publication number
WO2015068261A1
WO2015068261A1 PCT/JP2013/080242 JP2013080242W WO2015068261A1 WO 2015068261 A1 WO2015068261 A1 WO 2015068261A1 JP 2013080242 W JP2013080242 W JP 2013080242W WO 2015068261 A1 WO2015068261 A1 WO 2015068261A1
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WO
WIPO (PCT)
Prior art keywords
content
less
flux
cored wire
mass
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Ceased
Application number
PCT/JP2013/080242
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English (en)
Japanese (ja)
Inventor
熊谷　達也
修一 中村
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Nippon Steel Corp
Original Assignee
Nippon Steel and Sumitomo Metal Corp
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Nippon Steel and Sumitomo Metal Corp filed Critical Nippon Steel and Sumitomo Metal Corp
Priority to PCT/JP2013/080242 priority Critical patent/WO2015068261A1/fr
Priority to BR112015029349-2A priority patent/BR112015029349B1/pt
Priority to JP2014553365A priority patent/JP5696824B1/ja
Priority to CN201480030521.XA priority patent/CN105339132B/zh
Priority to KR1020157033517A priority patent/KR101655057B1/ko
Priority to CA2915026A priority patent/CA2915026C/fr
Priority to PCT/JP2014/070878 priority patent/WO2015068443A1/fr
Priority to AU2014345139A priority patent/AU2014345139B2/en
Priority to MYPI2015704221A priority patent/MY158148A/en
Priority to CA2926569A priority patent/CA2926569C/fr
Priority to MX2015017087A priority patent/MX352525B/es
Publication of WO2015068261A1 publication Critical patent/WO2015068261A1/fr
Priority to PH12015502625A priority patent/PH12015502625B1/en
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
    • 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
    • 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
    • B23K35/0222—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in soldering, brazing
    • B23K35/0244—Powders, particles or spheres; Preforms made therefrom
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
    • B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
    • B23K35/0261—Rods, electrodes, wires
    • B23K35/0266—Rods, electrodes, wires flux-cored
    • 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
    • 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
    • B23K35/306—Fe as the principal constituent with C as next major constituent, e.g. cast iron
    • 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
    • B23K35/3066—Fe as the principal constituent with Ni 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 degrees 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 degrees C
    • B23K35/3053—Fe as the principal constituent
    • B23K35/308—Fe as the principal constituent with Cr as next major constituent
    • B23K35/3086—Fe as the principal constituent with Cr as next major constituent containing Ni or Mn
    • 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
    • B23K35/3093—Fe as the principal constituent with other elements as next major constituents
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/3601—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest 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, 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, 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
    • B23K35/3603—Halide salts
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/3601—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest with inorganic compounds as principal constituents
    • B23K35/3603—Halide salts
    • B23K35/3605—Fluorides
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
    • B23K35/368—Selection of non-metallic compositions of core materials either alone or conjoint with selection of soldering or welding materials

Definitions

  • the present invention has a weld metal that has high hardness, excellent wear resistance, and is resistant to low-temperature cracking when welding high-hardness steel plates with excellent wear resistance used in the construction machinery and industrial machinery fields.
  • the present invention relates to a method for manufacturing a welded joint.
  • Steel plates used for construction machinery for excavation and civil engineering work in mines have many components that need to be replaced due to wear, but in order to extend their service life, wear-resistant steel with increased hardness of the steel plate Is used.
  • the hardness of the steel sheet varies depending on the environment and purpose of use, but in general, it is HB400 grade (Brinell hardness standard value HB360 to HB440, Vickers hardness standard value HV380 to HV469), HB450 grade (Brinell hardness) Standard values of HB410 to HB490, Vickers hardness standard value of HV435 to HV533), HB500 class (Brinell hardness standard value of HB450 to HB550, Vickers hardness standard value of HV478 to HV585) or HB600 class ( Abrasion-resistant steel sheets having a standard value of Brinell hardness of HB550 to HB650 and a standard value of Vickers hardness of HV585 to HV693) are often used.
  • the weld metal may be required to have wear resistance close to that of the base material (wear-resistant steel).
  • the base material wear-resistant steel
  • it is also necessary to increase its hardness.
  • the hardness of the weld metal is increased, low temperature cracks caused by hydrogen that enters during welding are very likely to occur.
  • the wear-resistant steel having high hardness is used as a base material, the strengthening of restraint is also one of the reasons that low temperature cracking is likely to occur.
  • preheating is generally performed prior to welding.
  • the hardness may decrease due to excessive heating temperature, so a very high preheating temperature is taken. I can't.
  • the wear resistance of the weld metal is also required, and the hardness of the weld metal is preferably equal to that of the base metal.
  • the hardness of the weld metal is at least HV380 or more.
  • the weld metal part what is important from the viewpoint of wear resistance is the hardness near the surface.
  • the weld metal in the lower layer is reheated by subsequent passes, so that the hardness is slightly reduced.
  • the weld metal in the uppermost layer is used. It is sufficient that the vicinity of each surface of the metal has sufficient hardness. From the above, in a welded joint using a high-hardness wear-resistant steel having a hardness of HV380 or more and HV693 or less as a base material, the surface hardness is HV380 or more and HV533 or less and having sufficient wear resistance, A welding method that forms a weld metal that does not cause cold cracking without preheating would be extremely useful.
  • Patent Documents 1 to 5 have been proposed as techniques for suppressing the low-temperature cracking caused by hydrogen generated in a high-strength weld metal.
  • patent document 1 prevents generation
  • Patent Document 2 prevents the occurrence of cold cracking by causing an oxide to function as a hydrogen trap site for a steel sheet that is also used for applications such as a high-strength line pipe.
  • Patent Document 3 prevents the occurrence of cold cracking by making Mo carbide function as a trap site for a steel material having a tensile strength of 800 to 1150 MPa.
  • Patent Document 4 discloses that the amount of diffusible hydrogen in the weld metal immediately after welding is reduced to about 3.0 to 4.0 ml / 100 g by adding an appropriate amount of Mg to the coating material of the coated arc welding material, thereby increasing the tensile strength. This is to improve the low temperature crack resistance of a steel material of 880 to 1180 MPa.
  • Patent Document 5 is a technique for suppressing low-temperature cracking by limiting the amount of hydrogen contained in a flux-cored wire for gas shielded arc welding.
  • an austenitic stainless steel welding material when used, the penetration of hydrogen into the weld metal is greatly reduced, so that the low temperature cracking susceptibility can be lowered. Moreover, since it is an austenite structure, a ductile fall cracking is hard to produce. However, a weld metal using an austenitic stainless steel welding material is not easy to increase strength, that is, hardness, and cannot be expected to have wear resistance.
  • the surface hardness is HV380 or higher and HV533 or lower, and it has excellent wear resistance and low temperature cracking. It is required to form a weld metal that is not easily generated by gas shield arc welding.
  • An object of the present invention is a welded joint using a high-hardness steel plate having a high C content and a surface hardness of HV380 or more and HV693 or less as a base material, and the surface hardness is HV380 or more and HV533 or less.
  • An object of the present invention is to provide a method for manufacturing a welded joint having a weld metal that has excellent wear resistance and is less susceptible to low temperature cracking.
  • the preheating temperature at the time of welding was important to prevent low temperature cracking, so it was common to weld with the preheating temperature as the top priority with a welding material for mild steel. Therefore, the problem was that the hardness of the weld metal part was low and wear was very likely to occur.
  • the present invention has newly found that when the hardness of the weld metal part is increased, the weld metal itself is very susceptible to cracking, not the heat-affected part of the base material. Therefore, after investigating the relationship between weld metal CEN and cracks, we found the appropriate range of weld metal CEN.
  • FIG. 1 shows that the y-type weld cracking test specified in JIS Z3158 was carried out under various conditions with various steel sheets and welding materials with different flux compositions, etc. It is the result of having produced the weld metal which has the amount of diffusible hydrogen, and calculated
  • FIG. 1 shows the relationship between the amount of diffusible hydrogen in the weld metal and the limit preheating temperature at which cracking is suppressed, organized according to the hardness level of the weld metal.
  • the low-temperature cracking test was conducted at room temperature (25 ° C.) in accordance with JIS Z3158 (y-type weld cracking test method: 1993), and was accepted as having passed on the surface and the cross section.
  • the measurement test of the amount of diffusible hydrogen was carried out by a gas chromatograph method based on JIS Z3118 (method for measuring the amount of hydrogen in steel welds; 2007).
  • the limit preheating temperature for the occurrence of cold cracking does not depend much on the hardness of the weld metal,
  • the cold cracking susceptibility of a weld metal having a hardness of HV380 or higher and HV533 or lower can be greatly reduced.
  • the amount of diffusible hydrogen in the weld metal immediately after welding up to this level has not been easy with the prior art.
  • the inventors have made various studies and have newly found that the amount of diffusible hydrogen in the weld metal can be stably reduced to a level that has been difficult in the past by improving the flux composition of the flux-cored wire. .
  • a certain amount of fluoride such as CaF 2 is contained in the flux component, the amount of oxide is adjusted, and the compounding ratio of fluoride and oxide is kept within a certain range.
  • the amount of diffusible hydrogen can be stably suppressed to less than 1.0 ml / 100 g.
  • Low-temperature cracking susceptibility of weld metal depends greatly on the hardness of the weld metal, but is also affected by alloying elements.
  • the inventors investigated the relationship between various alloy compositions and cold cracking susceptibility (cracking suppression preheating temperature) of weld metals of HV380 or higher and HV533 or lower.
  • the low temperature cracking test is conducted in accordance with JIS Z3158 (y-type weld cracking test method: 1993), and the minimum preheating temperature that does not cause low temperature cracking by changing the preheating temperature is determined as the crack initiation limit preheating temperature. did.
  • the flux-cored welding wire of the present invention described below is used, and the amount of diffusible hydrogen in the weld metal is less than 1.0 ml / 100 g.
  • the present invention has been made on the basis of the above findings, and the gist thereof is as follows.
  • the Vickers hardness HV is 380 to 514
  • the plate thickness is 20 to 100 mm
  • the C content is 0.12 to 0 .30%
  • the CEN calculated by the following formula 1 is 0.20 to 0.75%
  • the Vickers hardness HV is more than 514 and less than 565
  • the plate thickness is 12 to 100 mm.
  • Steel sheet with C content of 0.12 to 0.30%, CEN calculated by the following formula 1 is 0.20 to 0.75%, Vickers hardness HV is more than 565 and less than 693
  • the flux-cored wire contains at least one of CaF 2 , BaF 2 , SrF 2 , and MgF 2 and the total content is ⁇ , the ⁇ is based on the total mass of the flux-cored wire.
  • ⁇ is from 0.10 to 1.50 percent by mass% relative to the total weight of the flux-cored wire, CaCO 3, a total of BaCO 3, the content of SrCO 3, MgCO 3 is the flux incident Less than 0.60% by mass% with respect to the total mass of the wire, the content of iron powder in said flux is less than 10% by weight percent relative to the total weight of the flux-cored wire, the relative said alpha CaF 2
  • the ratio of ⁇ to ⁇ is 3.0 or more and 80.0 or less, and the content of CaO is 0 by mass% with respect to the total mass of the flux-cored wire.
  • the chemical composition is in mass% with respect to the total mass of the flux-cored wire: C: 0.06-0.35%; Si : 0.05 to 1.8%; Mn: 0.5 to 4.0%; P: 0.05% or less; S: 0.02% or less; Al: 0.005 to 0.15%; Cu: 0 to 0.75%; Ni: 0 to less than 1.0%; Cr: 0 Mo: 0 to 1.5%; Ti: 0 to 0.15%; Nb: 0 to 0.15%; V: 0 to 0.45%; B: 0 to 0.050%; Mg: 0 to 2.0%; Ca: 0 to 2.0%; REM: 0 to 0.0150%; balance: Fe and impurities; (c) the chemical composition of the weld metal of the weld joint is In mass%: C: 0.12-0.25%; Si: 0.05-0.80%; Mn: 0.2-2.5%; Al: 0.005-0.10%; P:
  • the Vickers hardness HV is more than 565 and not more than 693
  • the plate thickness is 12 to 20 mm
  • the C content is 0.35 to 0. .45%
  • CEN calculated by the following formula 2 is 0.20 to 0.85%
  • Vickers hardness HV is more than 565 and less than 693
  • plate thickness is more than 20 mm and less than 50 mm
  • C is 0.35 to 0.45%
  • CEN calculated by the following formula 2 is 0.20 to 0.85%.
  • a method of manufacturing a welded joint by performing gas shielded arc welding using a flux-cored wire with an outer shell filled with flux wherein (a) the thickness of the steel sheet is 20 mm during the gas shielded arc welding.
  • the steel sheet Perform preheating, the plate thickness of the steel plate of 20mm greater than the steel sheet subjected to pre-heating at least 0.99 ° C.
  • the flux-cored wire of CaF 2, BaF 2, SrF 2 , MgF 2
  • ⁇ is 3.3 to 8.0% by mass with respect to the total mass of the flux-cored wire
  • Ti oxide, Si oxide , Mg oxide, Al oxide at least one of them, and the total content is ⁇ , where ⁇ is 0.10 to 1.50 in mass% with respect to the total mass of the flux-cored wire.
  • the less than 10% in percentage by weight relative to the total weight of the flux cored wire, the ratio of the content of the CaF 2 with respect to the ⁇ is not less than 0.90, 80 wherein the ratio of ⁇ is 3.0 or more for the ⁇ 0.02 or less, the content of CaO is less than 0.20% by mass with respect to the total mass of the flux-cored wire, and the chemical components excluding metal fluoride, metal oxide, and metal carbonate are: In mass% with respect to the total mass of the flux-cored wire: C: 0.06 to 0.35%; Si: 0.05 to 1.8%; Mn: 0.5 to 4.0%; P: 0.05 S: 0.02% or less; Al: 0.005 to 0.15%; Cu: 0 to 0.75%; Ni: 0 to less than 1.0%; Cr
  • the content of the CaO in the flux-cored wire is 0.15% or less by mass% with respect to the total mass of the flux-cored wire. It may be.
  • the alloy may have a chemical composition in mass% with respect to the total mass of the flux-cored wire: Ni: 0 to 0.1%.
  • the steel outer shell may have a seamless shape.
  • perfluoropolyether oil may be applied to the surface of the flux-cored wire.
  • the surface hardness is HV380 or more and HV533 or less. Therefore, it is possible to obtain a welded joint that is excellent in wear resistance and hardly causes cold cracking.
  • the inventors In a welded joint using a high-hardness steel plate as a base material, the inventors, as described above, have a cold crack initiation limit preheating temperature if the amount of diffusible hydrogen in the weld metal immediately after welding is less than 1.0 ml / 100 g. Has found that it does not depend much on the hardness of the weld metal and can greatly reduce the low temperature cracking susceptibility of weld metals having a hardness of HV380 or more and HV533 or less.
  • the inventors have repeatedly studied various combinations and combinations of flux components of the flux-cored wire in order to reduce the amount of diffusible hydrogen in the weld metal immediately after welding to less than 1.0 ml / 100 g. It was.
  • fluorides such as CaF 2 are particularly effective in reducing hydrogen.
  • the amount of diffusible hydrogen in the weld metal can be greatly reduced.
  • By adjusting the amount and keeping the blending ratio of fluoride and oxide within a certain range it has been found that it can be stably suppressed to less than 1.0 ml / 100 g.
  • the present invention has been made based on such studies. Hereinafter, one mode of a manufacturing method of a welded joint of the present invention is explained.
  • the present invention uses, as a base material, a high-hardness thick steel plate having a C content of 0.12 to 0.45% by mass, HV380 or more and HV693 or less, which is widely used as a wear-resistant steel plate.
  • the target is a welded joint formed by gas shielded arc welding.
  • the weld metal has the chemical composition described in (1) or (2) above.
  • the reason for limiting the chemical composition of the weld metal will be described. In the following description, “%” means “% by mass” unless otherwise specified.
  • C is an element that most affects the hardness of the weld metal.
  • the base metal hardness is HV380 or more
  • the surface hardness of the weld metal is HV380 or more in order to ensure wear resistance close to that of the base material.
  • the C content of the weld metal needs to be 0.12% or more.
  • the upper limit of the C content is set to 0.25%.
  • the lower limit of the C content may be 0.13% or 0.14%.
  • the upper limit of the C content may be 0.23% or 0.21%.
  • Si 0.05-0.80%
  • Si is a deoxidizing element, and a certain amount is added to the flux in order to reduce the amount of O of the weld metal and increase the cleanliness. Therefore, the Si content in the weld metal is also 0.05% or more. If necessary, the lower limit of the Si content may be 0.10%, 0.15%, or 0.20%. If Si is contained in an amount exceeding 0.80%, the toughness of the weld metal may be deteriorated, so this is the upper limit. In order to improve the toughness of the weld metal, the upper limit of the Si content may be 0.70%, 0.65%, 0.60%, or 0.50%.
  • Mn 0.2-2.5% Since Mn has the effect of forming MnS and suppressing grain boundary embrittlement due to S, it is contained in the weld metal at least 0.2% or more. Further, since Mn is an element that has the effect of ensuring the hardenability of the weld metal and increasing the strength, it is desirable to contain 0.5% or more in order to stably obtain the hardness. In order to improve the hardness of the weld metal, the lower limit of the Mn content may be 0.6%, 0.7%, 0.8%, or 0.9%. On the other hand, if Mn exceeds 2.5%, the grain boundary embrittlement susceptibility increases and the toughness of the weld metal deteriorates, so this is the upper limit. In order to improve the toughness of the weld metal, the upper limit of the Mn content may be limited to 2.3%, 2.1%, 1.9%, 1.7%, or 1.5%.
  • Al 0.005 to 0.10%
  • Al is a deoxidizing element and, like Si, is effective in reducing the amount of O in the weld metal and improving the cleanliness, so it is necessary to add a certain amount to the flux.
  • the upper limit of the Al content may be limited to 0.09%, 0.08%, 0.07%, or 0.06%.
  • P 0.05% or less
  • the P content of the weld metal is limited to 0.05% or less as a range in which an adverse effect on toughness can be tolerated.
  • the upper limit of the P content may be limited to 0.03%, 0.025%, 0.02%, or 0.015%.
  • the lower limit of the P content is 0%.
  • S is also an impurity element, and if it is excessively present in the weld metal, it deteriorates both toughness and ductility, so it is preferable to reduce it as much as possible.
  • the S content of the weld metal is limited to 0.02% or less. If necessary, the upper limit of the S content may be limited to 0.015%, 0.01%, 0.008%, or 0.006%. There is no need to limit the lower limit of the S content. The lower limit of the S content is 0%.
  • N 0.015% or less
  • the N content is limited to 0.015% or less as an upper limit that can allow an influence on the weld metal. If necessary, the upper limit of the N content may be limited to 0.01%, 0.008%, or 0.006%. There is no need to limit the lower limit of the N content.
  • the lower limit of the N content is 0%.
  • O is inevitably contained in the weld metal, but the O content of the weld metal is limited to 0.100% or less as a range in which an adverse effect on toughness and ductility can be tolerated.
  • the upper limit of the O content may be 0.080%, 0.060%, 0.050%, or 0.040%.
  • the lower limit of the O content is 0%.
  • Cu (Cu: 0 to 0.5%) Since Cu can improve the strength and toughness of the weld metal, it can be contained as a selective element. However, if the Cu content exceeds 0.5%, the toughness may decrease, so the Cu content of the weld metal is set to 0.5% or less. If necessary, the upper limit of the Cu content may be 0.4% or 0.3%. There is no need to limit the lower limit of the Cu content. For this reason, the minimum of Cu content is 0%. On the other hand, in order to obtain a sufficient reinforcing effect, the weld metal may be contained in an amount of 0.1% or more. As a method for incorporating Cu into the weld metal, there are a method of plating the outer surface of the wire, or a method of adding it as a simple substance or an alloy element to the flux.
  • Ni Ni can be contained as a selective element that is effective for improving toughness.
  • the C content is high, the effect is limited and it is an expensive element, so the Ni content in the weld metal is less than 0.7%.
  • the upper limit of the Ni content may be 0.6%, 0.4%, or 0.2%.
  • the lower limit of the Ni content is 0%.
  • 0.05% or more may be contained in the weld metal.
  • Cr 0 to 2.5%) Cr is an element effective for improving the hardness of the weld metal by increasing the hardenability, and can be contained as a selective element. However, if over 2.5% is included, toughness may be reduced, so the Cr content is limited to 2.5%. If necessary, the upper limit of the Cr content may be 1.5%, 1.0%, 0.7%, or 0.4%. There is no need to limit the lower limit of the Cr content. For this reason, the lower limit of the Cr content is 0%. On the other hand, when it is added for the purpose of improving the hardness of the weld metal, it may be contained by 0.1% or more in order to obtain the effect.
  • Mo is an element effective for improving the hardness of the weld metal by increasing the hardenability, and can be contained as a selective element. However, if it exceeds 1.0% and it is excessively contained, the toughness may be lowered, so the upper limit of the Mo content is 1.0%. If necessary, the upper limit of the Mo content may be 0.7%, 0.6%, 0.4%, or 0.2%. There is no need to limit the lower limit of the Mo content. For this reason, the lower limit of the Mo content is 0%. On the other hand, when added for the purpose of improving the hardness, 0.05% or more may be contained in order to obtain the effect.
  • Ti is effective as a deoxidizing element, has an effect of reducing the amount of O in the weld metal, and can be contained as a selective element. It is also effective for fixing solute N and mitigating the adverse effect on toughness.
  • the Ti content in the weld metal exceeds 0.10% and becomes excessive, it forms coarse oxides. Since the possibility of toughness deterioration due to excessive toughening due to excessive precipitation strengthening increases, the upper limit of the Ti content is set to 0.10%. If necessary, the upper limit of the Ti content may be 0.08%, 0.05%, 0.03%, or 0.02%. There is no need to limit the lower limit of the Ti content. For this reason, the lower limit of the Ti content is 0%. For the purpose of improving toughness, 0.01% or more may be contained.
  • Nb has the effect of improving the hardness of the weld metal by solid solution, and can be contained as a selective element. However, if it exceeds 0.10%, it is not preferable because it is excessively contained in the weld metal and coarse precipitates are formed to deteriorate toughness, so the upper limit of Nb content is 0.10%. To do. If necessary, the upper limit of the Nb content may be 0.08%, 0.05%, 0.03%, or 0.02%. There is no need to limit the lower limit of the Nb content. For this reason, the lower limit of the Nb content is 0%. You may make it contain 0.01% or more for the purpose of the hardness improvement of a weld metal.
  • V is an element effective for improving the hardness of the weld metal by increasing the hardenability, and can be contained as a selective element. However, if the content exceeds 0.30%, the toughness may be lowered, so the V content is 0.30% as the upper limit. As needed, it is good also considering the upper limit of V content as 0.25%, 0.20%, or 0.15. There is no need to limit the lower limit of the V content. For this reason, the lower limit of the V content is 0%. You may make it contain 0.01% or more for the hardness improvement of a weld metal.
  • B (B: 0 to 0.0100%)
  • B has an effect of forming a BN in combination with the solid solution N and reducing the adverse effect on the toughness of the solid solution N.
  • B also has the effect of enhancing the hardenability and contributing to the strength improvement, and can be contained as a selective element. In order to obtain these effects, 0.0003% or more may be contained.
  • the upper limit of the B content when B is contained is 0.0100%. If necessary, the upper limit of the B content may be 0.0080%, 0.0060%, 0.0040%, or 0.0020%. There is no need to limit the lower limit of the B content, and the lower limit of the B content is 0%.
  • Mg 0-0.10%
  • Mg is a strong deoxidizing element, and may be contained in an amount of 0.001% or more in order to reduce the amount of O in the weld metal and improve the ductility and toughness of the weld metal.
  • Mg content in the weld metal exceeds 0.10%, a decrease in toughness due to the formation of coarse oxides in the weld metal cannot be ignored. For this reason, also when it contains Mg, Mg content shall be 0.10% or less.
  • the upper limit of the Mg content may be 0.0080%, 0.0060%, 0.0040%, or 0.0020%.
  • Ca and REM are effective in improving the ductility and toughness by changing the structure of the sulfide in the weld metal and reducing the size of the sulfide and oxide. You may contain REM 0.0002% or more. On the other hand, if it is excessively contained, it causes coarsening of sulfides and oxides, leading to deterioration of ductility and toughness. Therefore, the upper limit of the inclusion is 0.10% for Ca and 0.0100% for REM. To do.
  • the weld metal containing the above chemical composition may contain impurities mixed in the manufacturing process or the like as long as the balance containing iron as a main component does not impair the characteristics of the present invention.
  • CEN 0.20 to 0.58%
  • the crack initiation limit preheating temperature is 25 ° C. or less, and welding without preheating becomes possible.
  • the upper limit of CEN may be set to 0.55%, 0.53%, 0.50%, 0.47%, or 0.45%.
  • the lower limit of CEN is set to 0.20%.
  • the Vickers hardness HV of the base material is 380 or more and 514 or less (corresponding to HB 360 or more and 475 or less), the thickness of the base material is 20 to 100 mm, and the C content of the base material is 0.12 to A base material that is 0.30% and that has a CEN calculated by Equation 1 of 0.20 to 0.75%.
  • the Vickers hardness HV of the base material is 514 to 565 or less (corresponding to HB 475 to 530 or less), the base material has a thickness of 12 to 100 mm, and the C content of the base material is 0.12 to A base material that is 0.30% and that has a CEN calculated by Equation 1 of 0.20 to 0.75%.
  • the base material has a Vickers hardness HV of over 565 to 693 (corresponding to HB 530 of over 650 or less), the base material has a thickness of 8 to 12 mm, and the base material has a C content of 0.35 to A base material that is 0.45% and that has a CEN calculated by Equation 1 of 0.20 to 0.85%.
  • the base metal temperature satisfying any one of the above (a) to (c) is 10 ° C. or higher during gas shielded arc welding, it is not necessary to perform preheating work during welding.
  • the upper limit of the base material temperature (preheating temperature) is not particularly required, but may be less than 75 ° C or less than 50 ° C.
  • the base material has a Vickers hardness HV of more than 565 and less than 693 (corresponding to more than HB 530 and less than 650), the thickness of the base material is 12 to 20 mm, and the C content of the base material is 0.35 to A base material that is 0.45% and that has a CEN calculated by Equation 1 of 0.20 to 0.85%.
  • the Vickers hardness HV of the base material is more than 565 and less than or equal to 693 (corresponding to more than HB 530 and less than 650), the thickness of the base material is more than 20 mm and less than 50 mm, and the C content of the base material is 0.35
  • the base material is preheated to 100 ° C. or more, and the thickness of the base material is In the case of over 20 mm, the base material is preheated to 150 ° C. or higher.
  • the upper limit of the base material temperature is not particularly required, but may be less than 175 ° C or less than 150 ° C.
  • CEN is made 0.20% or more in order to make HV380 or more.
  • CEN [C] + (0.75 + 0.25 ⁇ tanh (20 ⁇ ([C] ⁇ 0.12))) ⁇ ([Si] / 24 + [Mn] / 6 + [Cu] / 15 + [Ni] / 20 + ([Cr] + [Mo] + [Nb] + [V]) / 5 + 5 ⁇ [B]) (Formula 1)
  • the element with [] represents the content (% by mass) of each element.
  • the average Vickers hardness of 1 mm below the outermost surface of the weld metal is HV380 to HV533, and the amount of diffusible hydrogen immediately after welding is less than 1.0 ml / 100 g. If the hardness at a position of 1 mm below the surface is HV380 or more and HV533 or less, the requirement for wear resistance required for the weld metal is satisfied. If it is less than HV380, the wear resistance is insufficient. If it exceeds HV533, cold cracking is likely to occur.
  • the hardness is measured by cutting a cross section perpendicular to the welding direction in a weld metal, collecting a polished sample, measuring 10 points of Vickers hardness at a position 1 mm below the surface of the weld metal, and calculating an average value. Shall be determined by
  • the amount of diffusible hydrogen in the weld metal immediately after welding is less than 1.0 ml / 100 g. It does not depend much on the hardness, and the low-temperature cracking susceptibility of a weld metal having a hardness of HV380 or more and HV533 or less can be greatly reduced.
  • the amount of diffusible hydrogen is measured by a gas chromatographic method based on JIS Z 3118 (Method for measuring the amount of hydrogen in steel welds; 2007). Since the diffusion rate of hydrogen is relatively high at room temperature, the amount of diffusible hydrogen in the weld metal must be measured immediately after welding. For this reason, unless it measures immediately after welding, the amount of diffusible hydrogen cannot be measured correctly.
  • a welded joint having a weld metal As described above, a high-hardness thick steel plate to be welded is used as a base material, and, for example, the two base materials are set at a welding position so as to form a groove therebetween. Then, by performing gas shielded arc welding using a flux-cored welding wire and generating a weld metal between the base materials, a weld joint composed of the weld metal and base metal plates on both sides thereof is formed.
  • steel plates, flux-cored welding wires, welding conditions and the like used for forming the weld metal will be described.
  • a high-hardness thick steel plate having a C content of 0.12% or more and 0.45% or less and HV380 or more and HV693 or less in mass% is an object.
  • the plate thickness of the steel plate to be used the thickness of 6 mm or more and 100 mm or less, which is generally referred to as a thick plate, is targeted.
  • Steel sheets satisfying such conditions are widely used in places where wear resistance is required, such as machinery for civil engineering and construction work, and there is no particular limitation on the chemical composition other than the C content.
  • C 0.12 to 3.0%, Si: 0.10 to 0.55%, Mn: 0.2 to 2.0%, Al: 0.01 to 0.10%, P: 0.02%
  • S 0.015% or less
  • Cu 0.5% or less
  • Cr 1.2% or less
  • Mo 0.6% or less
  • Nb 0.05% or less
  • CEN calculated by Equation 1 is 0.20 to 0.85%.
  • the upper limit of CEN is set to 0.85%.
  • the upper limit of CEN is set to 0.80%, 0.75%, 0.73, 0.70%, 0.68%, 0.65%,. It may be 63% or 0.60%.
  • the lower limit of CEN is set to 0.20%.
  • the lower limit of CEN may be 0.24%, 0.28%, 0.30%, 0.32%, 0.35%, or 0.38%.
  • a steel sheet having a base metal hardness of HV565 or less generally has a CEN of less than 0.75%.
  • the upper limit of CEN of a steel sheet having a base metal hardness of HV565 or less is set to 0.75%.
  • the method for measuring the hardness of the base material is a method in which five or more Vickers hardnesses at a position 1 mm below the surface of the cross section in the thickness direction of the base material are measured to obtain an average value.
  • the flux-cored welding wire to be used will be described separately for the flux component and the alloy component.
  • content of the component in description about a flux cored welding wire represents the mass% with respect to the total mass of a flux cored welding wire.
  • one or more kinds of (Al 2 O 3 ) metal oxides are contained in the welding wire in a certain amount, and the ratio of the fluoride to the oxide is within a certain range.
  • the amount of diffusible hydrogen can be stably reduced to less than 1.0 ml / 100 g.
  • the total amount ⁇ is 3.3% or more and 8.0% or less.
  • the total amount of Ti oxide, Si oxide, Mg oxide, and Al oxide is ⁇
  • the total amount ⁇ is 0.10% or more and 1.50% or less
  • the CaF with respect to ⁇ 2 is 0.90 or more
  • the ratio of the total amount ⁇ to the total amount ⁇ is 3.0 or more and 80.0 or less. Is a requirement.
  • the total amount ⁇ of the metal fluoride contained is less than 3.3%, the amount of diffusible hydrogen in the weld metal cannot be stably reduced to less than 1.0 ml / 100 g.
  • the lower limit of the total amount ⁇ may be 3.5%, 3.7%, or 3.9%.
  • the upper limit of the total amount ⁇ may be 7.5%, 7.0%, 6.5%, 6.0%, or 5.7%.
  • the total amount ⁇ of the metal oxides contained is less than 0.10%, the shape of the weld bead may be deteriorated, and if it exceeds 1.50%, the toughness may be lowered.
  • the lower limit of the total amount ⁇ may be 0.20%, 0.30%, 0.40%, or 0.50%.
  • the upper limit of the total amount ⁇ may be 1.30%, 1.20%, 1.10%, 1.00%, 0.90%, or 0.80%.
  • the ratio of the total amount ⁇ to the total amount ⁇ is less than 3.0, the amount of diffusible hydrogen in the weld metal cannot be stably reduced to less than 1.0 ml / 100 g, and if it exceeds 80.0 Since welding fume and slag are excessively generated, welding workability is remarkably lowered, which is not preferable.
  • the lower limit of the ratio ([total amount ⁇ ] / [total amount ⁇ ]) is set to 3.2, 3.5, 3.7, or 4.0. Also good.
  • the upper limit of the ratio ([total amount ⁇ ] / [total amount ⁇ ]) is set to 40.0, 30.0, 20.0, 15.0 or 13. It may be 0.
  • the ratio of the total amount ⁇ of metal fluoride to the total amount ⁇ of metal fluoride, the total amount ⁇ of metal oxide, and the total amount ⁇ of metal oxide is limited as described above.
  • the total amount ⁇ is the content in the flux-cored wire, and the total content is also included in binders (water glass containing SiO 2 as a main component) used for flux granulation. .
  • one or more of CaCO 3 , BaCO 3 , SrCO 3 , and MgCO 3 metal carbonates can be further added for the purpose of improving arc stability and arc concentration. If 0.60% or more is added, the concentration of the arc is too strong, the amount of spatter generated is large, and the amount of oxygen in the weld metal also increases. Therefore, when these metal carbonates are contained, the total content is less than 0.60%.
  • the lower limit of the total content of these metal carbonates is 0%.
  • the upper limit may be set to 0.50%, 0.40%, 0.20%, or 0.10% in order to suppress the amount of spatter generated.
  • metal fluoride reduces the amount of diffusible hydrogen is not necessarily clear, but was metal fluoride decomposed by a welding arc, and the generated fluorine combined with hydrogen and dissipated into the atmosphere as HF gas? Alternatively, it is considered that hydrogen is fixed as HF in the weld metal as it is.
  • CaO may be contained in the flux raw material.
  • the CaO content is limited to less than 0.20%. Preferably it is 0.15% or less or 0.10% or less. If the content is limited to less than 0.20%, the effect of the present invention can be obtained. Since CaO changes to CaOH when exposed to the atmosphere, it may increase diffusible hydrogen in the weld metal.
  • the amount of alloying elements in the flux-cored wire excluding metal fluorides, metal oxides, and metal carbonates is also limited as follows.
  • the C content in the flux-cored wire is less than 0.06%, the C content in the weld metal is less than 0.12%, so the C content in the flux-cored wire is 0.06% or more. .
  • the lower limit of the C content may be 0.07%, 0.08%, 0.09%, 0.10%, or 0.11%.
  • the C content in the flux-cored wire exceeds 0.35%, the C content in the weld metal exceeds 0.25%, so the C content in the flux-cored wire is 0.35% or less.
  • the upper limit of the C content may be 0.30%, 0.25%, 0.18%, 0.17%, or 0.16%.
  • the Si content in the flux-cored wire is less than 0.05%, the Si content in the weld metal is less than 0.05%, so the Si content in the flux-cored wire is 0.05% or more. .
  • the lower limit of the Si content may be 0.10%, 0.20%, 0.30%, or 0.40%. If the Si content in the flux-cored wire exceeds 1.8%, the Si content in the weld metal exceeds 0.80% even if oxidation consumption is taken into consideration, so the Si content in the flux-cored wire is 1 .8% or less.
  • the upper limit of the Si content may be 1.5%, 1.2%, 1.0%, 0.8%, or 0.6%.
  • Mn 0.5-4.0% If the Mn content in the flux-cored wire is less than 0.5%, the Mn content in the weld metal is less than 0.2%, so the Mn content in the flux-cored wire is 0.5% or more. . In order to improve the hardness of the weld metal, the lower limit of the Mn content may be 0.7%, 0.8%, 0.9%, 1.0%, or 1.1%. If the Mn content in the flux-cored wire exceeds 4.0%, the Mn content in the weld metal exceeds 2.5% even if oxidation consumption is taken into consideration, so the Mn content in the flux-cored wire is 4. 0% or less. In order to improve the toughness of the weld metal, the upper limit of the Mn content may be 3.0%, 2.5%, 2.2%, 2.0%, or 1.8%.
  • the P content in the flux-cored wire exceeds 0.05%, the P content in the weld metal may exceed 0.05%, so the P content in the flux-cored wire is 0.05%.
  • the upper limit of the P content may be limited to 0.03%, 0.025%, 0.02%, or 0.015%.
  • the lower limit of the P content is 0%.
  • the S content in the flux-cored wire exceeds 0.02%, the S content in the weld metal may exceed 0.02%, so the S content in the flux-cored wire is 0.02%.
  • the upper limit of the S content may be limited to 0.015%, 0.01%, 0.008%, or 0.006%.
  • the lower limit of the S content is 0%.
  • the Al content in the flux-cored wire is less than 0.005%, the Al content in the weld metal is less than 0.005%, so the Al content in the flux-cored wire is 0.005% or more. .
  • the lower limit of the Al content may be 0.007%, 0.010%, or 0.012%. If the Al content in the flux cored wire exceeds 0.15%, the Al content in the weld metal may exceed 0.10%, so the Al content in the flux cored wire is 0.15%.
  • the upper limit of the Al content may be limited to 0.09%, 0.07%, 0.05%, or 0.04%.
  • the Cu content in the flux-cored wire exceeds 0.75%, the Cu content in the weld metal exceeds 0.50%, so the Cu content in the flux-cored wire is 0.75% or less. .
  • the Cu content may be 0.5% or less.
  • the upper limit of the Cu content may be 0.4% or 0.3%.
  • the minimum of Cu content is 0%.
  • the weld metal may contain 0.1% or more of Cu.
  • the Ni content in the flux-cored wire is 1.0% or more
  • the Ni content of the weld metal becomes 0.7% or more, and the alloy cost of the wire increases. Therefore, the Ni content in the flux-cored wire is 1.0% or less.
  • the upper limit of the Ni content may be 0.5%, 0.4%, 0.3%, 0.2, or 0.1%.
  • the lower limit of the Ni content is 0%.
  • the Cr content in the flux-cored wire exceeds 3.5%, the Cr content in the weld metal exceeds 2.5%, so the Cr content in the flux-cored wire is 3.5% or less. .
  • the upper limit of the Cr content may be 1.5%, 1.0%, 0.5%, or 0.1%.
  • the lower limit of the Cr content is 0%.
  • 0.05% or more may be contained in order to obtain the effect.
  • Mo 0 to 1.5% If the Mo content in the flux-cored wire exceeds 1.5%, the Mo content in the weld metal exceeds 1.0%, so the Mo content in the flux-cored wire is 1.5% or less. .
  • the upper limit of the Mo content may be 0.7%, 0.5%, 0.3%, or 0.2%. There is no need to limit the lower limit of the Mo content. For this reason, the lower limit of the Mo content is 0%.
  • 0.05% or more may be contained in order to obtain the effect.
  • Ti 0 to 0.15% If the Ti content in the flux-cored wire exceeds 0.15%, the Ti content in the weld metal exceeds 0.10%, so the Ti content in the flux-cored wire is 0.15% or less. .
  • the upper limit of the Ti content may be 0.10%, 0.08%, or 0.05%. There is no need to limit the lower limit of the Ti content. For this reason, the lower limit of the Ti content is 0%. For the purpose of improving toughness, 0.01% or more may be contained.
  • the Nb content in the flux-cored wire exceeds 0.15%, the Nb content in the weld metal exceeds 0.10%, so the Nb content in the flux-cored wire is 0.15% or less. .
  • the upper limit of the Nb content may be 0.10%, 0.08%, or 0.05%.
  • the lower limit of the Nb content is 0%. You may make it contain 0.01% or more for the purpose of the hardness improvement of a weld metal.
  • V (V: 0 to 0.45%) If the V content in the flux-cored wire exceeds 0.45%, the V content in the weld metal exceeds 0.30%, so the V content in the flux-cored wire is 0.45% or less. .
  • the upper limit of the V content may be 0.25%, 0.20%, or 0.15. There is no need to limit the lower limit of the V content. For this reason, the lower limit of the V content is 0%. You may make it contain 0.01% or more for the hardness improvement of a weld metal.
  • the B content in the flux-cored wire exceeds 0.050%, the B content of the weld metal exceeds 0.0100%, so the B content in the flux-cored wire is 0.050% or less.
  • the upper limit of the B content may be 0.040%, 0.020%, 0.010%, or 0.005%. There is no need to limit the lower limit of the B content, and the lower limit of the B content is 0%.
  • the Mg content in the flux-cored wire exceeds 2.0%, the Mg content in the weld metal exceeds 0.10%, so the Mg content in the flux-cored wire is 2.0% or less. .
  • the upper limit of the Mg content may be 1.5%, 1.0%, 0.4%, or 0.2%. There is no need to limit the lower limit of the Mg content, and the lower limit of the Mg content is 0%.
  • the Ca content in the flux-cored wire exceeds 2.0%, the Ca content in the weld metal exceeds 0.10%, so the Ca content in the flux-cored wire is 2.0% or less. .
  • the upper limit of the Ca content may be 1.5%, 1.0%, 0.5%, or 0.3%. There is no need to limit the lower limit of the Ca content, and the lower limit of the Ca content is 0%.
  • the REM content in the flux-cored wire exceeds 0.0150%, the REM content in the weld metal exceeds 0.0100%, so the REM content in the flux-cored wire is 0.0150% or less.
  • the upper limit of the REM content may be 0.0100%, 0.0050%, or 0.0030%. There is no need to limit the lower limit of the REM content, and the lower limit of the REM content is 0%.
  • the above is the reason for limitation regarding the chemical composition of the flux-cored wire of the present invention.
  • the remaining alloy chemical components may contain impurities mixed in the manufacturing process or the like as long as the balance containing Fe as a main component does not impair the characteristics of the present invention.
  • the Fe component includes Fe in the steel outer shell, iron powder added in the flux, and Fe in the alloy component.
  • the content of iron powder in the flux is less than 10%. When there is much iron powder content, the amount of oxygen may increase. If necessary, the iron powder content may be less than 5% or less than 1%.
  • the flux-cored wires can be roughly classified into a seamless wire having no slit-like seam in the steel outer shell and a wire having a seam having a slit-like gap at the steel outer seam.
  • any cross-sectional structure can be adopted, but a seamless wire is preferable in order to suppress cold cracking of the weld metal.
  • Hydrogen that penetrates into the weld during welding diffuses into the weld metal and on the steel side, accumulates in the stress concentration part, and causes cold cracking.
  • This hydrogen source can increase moisture contained in the welding material, moisture mixed in from the atmosphere, rust and scale attached to the steel surface, etc., but under the welding where the cleanliness of the weld and the gas shield conditions are sufficiently controlled. Then, hydrogen mainly contained in water in the wire is a main factor of diffusible hydrogen existing in the weld joint.
  • the steel outer shell into a seamless tube, and to suppress the penetration of hydrogen in the atmosphere from the steel outer shell to the flux after the wire is manufactured and used.
  • moisture in the atmosphere easily enters the flux from the seam portion of the outer shell, and as it is, it cannot prevent the intrusion of a hydrogen source such as moisture. Therefore, when the period until use after production is long, the entire wire is preferably vacuum-packed or stored in a container that can be kept dry.
  • lubricating oil may be applied to the wire surface. From the viewpoint of reducing diffusible hydrogen, the lubricating oil applied to the wire surface is preferably an oil that does not contain hydrogen, such as perfluoropolyether (PFPE) oil.
  • PFPE perfluoropolyether
  • the flux cored wire used in the present invention can be manufactured by the same manufacturing process as that of a normal flux cored wire manufacturing method. That is, first, a steel strip to be an outer skin and a flux containing metal fluoride, an alloy component, a metal oxide, a metal carbonate, and an arc stabilizer are prepared so as to have predetermined contents. While feeding the steel strip in the longitudinal direction, it is formed into an open tube (U-shaped) with a forming roll to form a steel outer shell. During this forming, flux is supplied from the opening of the open tube, and the opposing edge surface of the opening is Butt seam welding. A seamless pipe obtained by welding is drawn and annealed during or after the drawing process to obtain a seamless wire having a desired wire diameter. Moreover, a part is made into the pipe
  • the present invention for the steel sheet, using a flux-cored wire that meets the above-mentioned conditions, by performing multi-layer welding by gas shield arc welding, and forming a weld metal that meets the above-described conditions,
  • the object can be achieved, and the method of gas shield arc welding is not particularly limited, and a commonly used method can be adopted.
  • the shielding gas in addition to 100% CO 2 gas, a mixed gas of Ar gas and 3 to 20 vol% CO 2 gas can be used.
  • the welding conditions such as current and voltage are, for example, a current of 200 to 350 A and a voltage of 25 to 35 V.
  • the welding speed may be controlled so that the welding heat input is 10 to 50 kJ / cm.
  • the shape of the welded joint to be manufactured is determined according to the application and is not particularly limited. It can be applied to welded joints that form grooves, such as ordinary butt joints, square joints, and T joints. Therefore, the shape of the steel plate to be welded is not limited as long as at least the portion forming the welded joint is plate-like, and the whole may not be a plate, and includes, for example, a shape steel. Moreover, it is not limited to what is comprised from a separate steel plate, The butt-welding joint of what shape
  • a steel plate having the components shown in Table 1 was used as a base material.
  • the same steel plate as the base material was used for the backing metal for welding. While forming the steel strip in the longitudinal direction, it is formed into an open tube with a forming roll, and flux is supplied from the opening of the open tube during the forming, and the opposite edge surfaces of the opening are butt seam welded to seamless pipe Then, annealing was performed in the course of drawing the piped wire, and a flux-cored wire having a final wire diameter of ⁇ 1.2 mm was made as a prototype.
  • a part of the pipe was a seam-welded pipe and was drawn to produce a flux-cored wire with a wire diameter of ⁇ 1.2 mm.
  • the analysis of the chemical composition of the prototype flux cored wire was performed as follows. First, the filled flux was taken out from the flux-cored wire, and the flux-cored wire was divided into a steel outer shell and a flux. The chemical component of the steel outer skin was determined by measuring the content of each metal component by chemical analysis. The flux was first quantitatively evaluated for constituents and components by X-ray diffraction and fluorescent X-ray analysis.
  • Tables 2-1 to 2-4 and Tables 3-1 to 3-4 show the chemical compositions of the trial-made flux cored wires.
  • the above-mentioned base material was abutted at a root gap of 16 mm and a groove angle of 20 °, and welding was performed using a backing metal under the welding conditions shown in Tables 4-1 to 4-3. .
  • the groove surface of the base material and the surface of the backing metal were subjected to buttering with two or more layers and a height of 3 mm or more using a flux-cored wire to be tested.
  • Ti oxide, Si oxide, Mg oxide, Al oxide respectively by using the TiO 2, SiO 2, MgO, Al 2 O 3.
  • the metal carbonates are CaCO 3 , BaCO 3 , SrCO 3 , and MgCO 3 .
  • the chemical composition analysis results of the obtained weld metal are shown in Table 5-1, Table 5-2, Table 5-4, Table 5-5, Table 5-7, and Table 5-8.
  • a sample obtained by polishing a cross section perpendicular to the welding direction was taken from this weld metal, measured at 10 points of Vickers hardness at a position 1 mm below the surface of the weld metal, and Brinell hardness from SAE J417 (1983) hardness conversion table. Converted to Further, a No. 4 Charpy test piece (2 mmV notch) based on JIS Z3111 (2005) was sampled, and the Charpy absorbed energy at ⁇ 40 ° C. of the weld metal was measured. A sample having an absorption energy of ⁇ 40 ° C. or more of 27 J or more was regarded as acceptable.
  • the obtained hardness and Charpy test results are shown in Tables 5-3, 5-6, and 5-9.
  • a low temperature cracking test and a diffusible hydrogen content measurement test were performed under the same welding conditions.
  • the low-temperature cracking test was conducted at room temperature (25 ° C.) in accordance with JIS Z3158 (y-type weld cracking test method: 1993).
  • the diffusible hydrogen content measurement test was carried out by a gas chromatograph method based on JIS Z3118 (Method for measuring the hydrogen content of steel welds; 2007). The results are shown in Table 5-3, Table 5-6, and Table 5-9.
  • the surface hardness is HV380 or more and HV533 or less and wear resistance. Since it is possible to obtain a weld metal having excellent properties without generating low-temperature cracks without preheating, the welding work efficiency can be remarkably improved, and the value in the industry is extremely high.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Chemical & Material Sciences (AREA)
  • Inorganic Chemistry (AREA)
  • Nonmetallic Welding Materials (AREA)
  • Butt Welding And Welding Of Specific Article (AREA)
  • Arc Welding In General (AREA)

Abstract

L'invention porte sur un procédé pour produire un joint soudé, lequel procédé comprend le fait de soumettre une plaque d'acier à un soudage à l'arc protégé par un gaz par l'utilisation d'un fil-électrode fourré, ladite plaque d'acier ayant une dureté Vickers HV de 380 à 514 inclus, une épaisseur de plaque de 20 à 100 mm, une teneur en C de 0,12 à 0,30 %, et un CEN de 0,20 à 0,75 %, ledit CEN étant calculé selon l'équation 1 suivante : CEN = [C]+(0,75+0,25×tanh(20×([C]-0,12)))×([Si]/24+[Mn]/6+[Cu]/15+[Ni]/20+([Cr]+[Mo]+[Nb]+[V])/5+5×[B]).
PCT/JP2013/080242 2013-11-08 2013-11-08 Procédé pour produire un joint soudé Ceased WO2015068261A1 (fr)

Priority Applications (12)

Application Number Priority Date Filing Date Title
PCT/JP2013/080242 WO2015068261A1 (fr) 2013-11-08 2013-11-08 Procédé pour produire un joint soudé
AU2014345139A AU2014345139B2 (en) 2013-11-08 2014-08-07 Method for producing weld joint
MYPI2015704221A MY158148A (en) 2013-11-08 2014-08-07 Method of producing weld joint
CN201480030521.XA CN105339132B (zh) 2013-11-08 2014-08-07 焊接接头的制造方法
KR1020157033517A KR101655057B1 (ko) 2013-11-08 2014-08-07 용접 조인트의 제조 방법
CA2915026A CA2915026C (fr) 2013-11-08 2014-08-07 Procede de production de raccord soude
PCT/JP2014/070878 WO2015068443A1 (fr) 2013-11-08 2014-08-07 Procédé de production de raccord soudé
BR112015029349-2A BR112015029349B1 (pt) 2013-11-08 2014-08-07 método para a produção de junta de solda
JP2014553365A JP5696824B1 (ja) 2013-11-08 2014-08-07 溶接継手の製造方法
CA2926569A CA2926569C (fr) 2013-11-08 2014-08-07 Procede de production de raccord soude
MX2015017087A MX352525B (es) 2013-11-08 2014-08-07 Método para producir una junta de soldadura.
PH12015502625A PH12015502625B1 (en) 2013-11-08 2015-11-25 Method for producing weld joint

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JP2018144071A (ja) * 2017-03-06 2018-09-20 新日鐵住金株式会社 ガスシールドアーク溶接用フラックス入りワイヤ及び溶接継手の製造方法
JP2022061854A (ja) * 2020-10-07 2022-04-19 日本製鉄株式会社 溶接継手の製造方法
CN116732421A (zh) * 2023-06-02 2023-09-12 北京科技大学 一种极寒环境用高强韧船体结构钢及其制备方法和应用

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US10946486B2 (en) 2016-03-08 2021-03-16 Nippon Steel Corporation Flux-cored wire, manufacturing method of welded joint, and welded joint
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US11400539B2 (en) 2016-11-08 2022-08-02 Nippon Steel Corporation Flux-cored wire, manufacturing method of welded joint, and welded joint
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WO2019186797A1 (fr) * 2018-03-28 2019-10-03 日本製鉄株式会社 Procédé de fabrication de fil fourré, fil fourré et procédé de fabrication d'un joint soudé
KR102272173B1 (ko) * 2018-03-28 2021-07-05 닛폰세이테츠 가부시키가이샤 플럭스 내포 와이어의 제조 방법, 플럭스 내포 와이어 및 용접 이음의 제조 방법
CN108588572A (zh) * 2018-07-27 2018-09-28 安徽卓煌机械设备有限公司 一种高强度易焊接磨辊基体材料
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US11701730B2 (en) * 2019-01-15 2023-07-18 Postle Industries, Inc. Nickel-containing stick electrode
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JP7143938B2 (ja) * 2019-03-27 2022-09-29 日本製鉄株式会社 自動車用足回り部品
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US20210229204A1 (en) * 2020-01-29 2021-07-29 Lincoln Global, Inc. Systems and methods for multi-wire submerged arc welding using a flux-cored wire electrode
CN112975197B (zh) * 2021-02-24 2023-02-21 天津市金桥焊材集团股份有限公司 一种高效焊接热锻压模具堆焊硬面层用药芯焊丝
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CN115041866A (zh) * 2022-06-30 2022-09-13 三一重机有限公司 气体保护焊丝及其在低合金高强钢的焊接中的应用
CN118742410A (zh) * 2022-12-21 2024-10-01 浦项股份有限公司 焊接构件和气体保护电弧焊用焊丝
KR102818628B1 (ko) * 2023-01-18 2025-06-10 주식회사 포스코 가스 실드 아크 용접용 와이어
EP4527542A1 (fr) * 2023-01-20 2025-03-26 POSCO Co., Ltd Métal de soudure à l'arc sous protection gazeuse

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JP2018144071A (ja) * 2017-03-06 2018-09-20 新日鐵住金株式会社 ガスシールドアーク溶接用フラックス入りワイヤ及び溶接継手の製造方法
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CN116732421A (zh) * 2023-06-02 2023-09-12 北京科技大学 一种极寒环境用高强韧船体结构钢及其制备方法和应用

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CA2926569A1 (fr) 2015-05-14
KR101655057B1 (ko) 2016-09-06
CA2915026C (fr) 2016-10-04
AU2014345139A1 (en) 2015-12-17
MX2015017087A (es) 2016-04-11
WO2015068443A1 (fr) 2015-05-14
KR20150136551A (ko) 2015-12-07
CN105339132A (zh) 2016-02-17
MY158148A (en) 2016-09-15
CA2915026A1 (fr) 2015-05-14
AU2014345139B2 (en) 2016-03-31
MX352525B (es) 2017-11-29
CN105339132B (zh) 2017-04-12
CA2926569C (fr) 2017-04-18

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