WO2012105617A1 - 耐水素脆化感受性に優れた溶接金属 - Google Patents
耐水素脆化感受性に優れた溶接金属 Download PDFInfo
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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
- B23K35/3093—Fe as the principal constituent with other elements as next major constituents
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/02—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape
- B23K35/0255—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by mechanical features, e.g. shape for use in welding
- B23K35/0261—Rods, electrodes, wires
- B23K35/0266—Rods, electrodes, wires flux-cored
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—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
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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
- B23K35/24—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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/02—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
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
Definitions
- the present invention relates to a weld metal having reduced sensitivity to hydrogen embrittlement in a weld metal used for a welded structure.
- gas shielded arc welding using a flux-cored wire has excellent welding workability, so a technique for ensuring low temperature cracking resistance is required for a weld metal formed by this welding method.
- Patent Document 1 discloses a technique for preventing low-temperature cracking by dispersing Mo carbide (carbide containing Mo) having a high hydrogen trap capability in a weld metal.
- Mo carbide carbide containing Mo
- Patent Document 1 discloses a technique for preventing low-temperature cracking by dispersing Mo carbide (carbide containing Mo) having a high hydrogen trap capability in a weld metal.
- this technique in order to disperse Mo carbides, it is necessary to employ a special welding technique in which the steel materials are butted and then submerged arc welding is performed from the inner surface side.
- Patent Document 2 proposes a technique for preventing cold cracking by managing the cooling time during welding. This technology requires strict construction management according to the components, and has a problem that the work load is high.
- Patent Document 3 proposes a technique for preventing cold cracking by setting the retained austenite fraction for trapping diffusible hydrogen to 1% or more in the weld metal.
- this technique is premised on double-sided one-pass seam welding in steel pipes, and cannot be applied to general welding of steel materials.
- Patent Document 4 proposes a technology for improving cold cracking resistance by reducing the amount of diffusible hydrogen and appropriately controlling the strength and chemical composition. However, even in this technique, since a satisfactory strength level is affected by the components, the number of application points is limited in actual construction.
- weld metals used for offshore structures Since these weld metals can withstand use in cold regions, high values are required not only for resistance to hydrogen embrittlement and strength, but also for low temperature toughness.
- Japanese Unexamined Patent Publication No. 2005-40816 Japanese Unexamined Patent Publication No. 2003-33876 Japanese Laid-Open Patent Publication No. 2002-115032 Japanese Unexamined Patent Publication No. 11-147196
- the present invention has been made in view of the above circumstances, and the purpose thereof is a weld metal that has excellent resistance to hydrogen embrittlement resistance even if it has high strength, and that does not cause cold cracking.
- the object is to provide a weld metal having excellent low-temperature toughness.
- the weld metal according to the present invention that has solved the above problems is a weld metal formed by gas shielded arc welding using a flux-cored wire, C: 0.02 to 0.12% (meaning “mass%”; chemical composition is the same hereinafter), Si: 0.10 to 2.0%, Mn: 0.90 to 2.5%, Ni : 0.20 to 3.5%, Mo: 0.05 to 1.5%, Ti: 0.040 to 0.150%, N: 0.015% or less (excluding 0%), and O: 0 0.030-0.10% each, the balance being iron and inevitable impurities, It has a gist in that there are 2500 / mm 2 or more of retained austenite particles and the total volume fraction of the retained austenite particles is 4.0% or more. In addition, the size of the retained austenite particles that are the objects in the measurement of the number density is not less than the measurement limit (the equivalent circle diameter exceeds 0.15 ⁇ m).
- the weld metal of the present invention satisfies Si: 0.10 to 0.5% and Ni: 1.0 to 2.0%, respectively, and the ⁇ value defined by the following formula (1) is 3.2. It is also useful to satisfy the above requirement, and as a result, a weld metal having excellent low-temperature toughness (specifically, impact absorption energy vE -40 at ⁇ 40 ° C. exceeds 85 J) can be realized.
- ⁇ value [Mn] + [Ni] + (2 ⁇ [Mo]) + (16 ⁇ [Ti]) ⁇ (12 ⁇ [O]) (1)
- [Mn], [Ni], [Mo], [Ti] and [O] indicate the contents (mass%) of Mn, Ni, Mo, Ti and O, respectively.
- oxide particles containing 20% by mass or more of Ti and having an equivalent circle diameter of 0.15 to 1.0 ⁇ m are present at 5000 / mm 2 or more.
- the “equivalent circle diameter” is a diameter of a circle that is assumed to have the same area by paying attention to the size of residual austenite particles and oxide particles observed on the observation surface of the optical microscope.
- the weld metal of the present invention as other elements, (a) Cr: 2.0% or less (not including 0%), V: 0.60% or less (not including 0%), Nb: 0 .1% or more selected from the group consisting of 15% or less (excluding 0%) and Cu: 1.0% or less (excluding 0%), (b) Al: 0.020% or less (0% And / or Zr: 0.10% or less (not including 0%), (c) B: 0.0050% or less (not including 0%), etc. Depending on the type, the properties of the weld metal are further improved.
- the number density of the retained austenite particles and the total volume fraction are appropriately controlled together with the chemical component composition, so that a weld metal with excellent resistance to hydrogen embrittlement can be realized.
- the weld metal has excellent low-temperature toughness by defining the contents of Si and Ni more strictly and satisfying a predetermined relational expression defined by the contents of Mn, Ni, Mo, Ti and O. Can be realized.
- the present inventors examined from various angles about the means for improving the resistance to hydrogen embrittlement in HT780 class high strength weld metal formed by gas shielded arc welding using flux-cored wire. As a result, it has been found that the formation of residual austenite particles acting as diffusible hydrogen trap sites at a predetermined density improves the resistance to hydrogen embrittlement resistance, thereby completing the present invention.
- the weld metal component is controlled within a predetermined range, the residual austenite particles existing in the weld metal are 2500 particles / mm 2 or more, and the total volume fraction of residual austenite particles (ratio to the entire structure) is 4.0%. It has been found that the hydrogen embrittlement resistance is improved in the HT780 class weld metal by the above control.
- the residual austenite particles present in the weld metal are 2500 particles / mm 2 or more, and the total volume fraction of the residual austenite particles is 4.0% or more, whereby the hydrogen trap effect. This reduced the hydrogen embrittlement susceptibility.
- the number of retained austenite particles is preferably 3000 / mm 2 or more (more preferably 3300 / mm 2 or more), and the total volume fraction of retained austenite particles is 4.5% or more. Preferred (more preferably 4.8% or more).
- ⁇ value [Mn] + [Ni] + (2 ⁇ [Mo]) + (16 ⁇ [Ti]) ⁇ (12 ⁇ [O]) (1)
- [Mn], [Ni], [Mo], [Ti] and [O] indicate the contents (mass%) of Mn, Ni, Mo, Ti and O, respectively.
- Mn, Ni, Mo and Ti constituting the ⁇ value of the above formula (1) have a function of suppressing the formation of grain boundary ferrite by being present in a solid solution state.
- Mn and Ti comprise an oxide, the amount which exists in a solid solution state will increase by reducing O. From these viewpoints, it was found that the coefficient of each element was experimentally obtained and the ⁇ value was set to 3.2 or more, whereby the formation of grain boundary ferrite was suppressed and the low temperature toughness was improved.
- C is an element indispensable for ensuring the strength of the weld metal, and in order to exert such an effect, it is necessary to contain 0.02% or more. Preferably it is 0.04% or more, More preferably, it is 0.06% or more. However, if the C content exceeds 0.12%, the strength increases excessively and the hydrogen embrittlement susceptibility increases (hydrogen embrittlement susceptibility deteriorates). In addition, the upper limit with preferable C content is 0.10%, More preferably, it is 0.08% or less.
- Si 0.10 to 2.0%
- Si exists in a solid solution state, thereby delaying carbide formation and stabilizing retained austenite. If the Si content is less than 0.10%, retained austenite cannot be secured.
- the content is preferably 0.25% or more, more preferably 0.28% or more.
- the Si content is excessive, the sensitivity to hydrogen embrittlement due to an excessive increase in strength increases, so it is necessary to suppress it to 2.0% or less. It is preferably 1.5% or less, and more preferably 0.5% or less.
- the Si content is preferably 0.5% or less (more preferably 0.4% or less). That is, when the Si content exceeds 0.5%, hard island martensite is formed, and this becomes a starting point of fracture, so that the low temperature toughness tends to deteriorate.
- Mn is an element necessary for ensuring the strength of the weld metal, and in order to exert such an effect, it is necessary to contain 0.90% or more. Preferably it is 1.2% or more, More preferably, it is 1.5% or more. However, if the content exceeds 2.5%, the hydrogen embrittlement susceptibility increases due to an excessive increase in strength. Preferably it is 2.2% or less, More preferably, it is 2.0% or less.
- Ni is an element necessary for ensuring the strength of the weld metal, and in order to exert such effects, it is necessary to contain 0.20% or more. Preferably it is 0.5% or more, More preferably, it is 1.0% or more. However, if it exceeds 3.5%, it causes excessive hydrogen embrittlement susceptibility due to an excessive increase in strength. Preferably it is 3.0% or less, More preferably, it is 2.8% or less. In particular, in order to improve the low temperature toughness of the weld metal, the Ni content is 1.0% or more and 2.0% or less (a more preferable lower limit is 1.1%, and a further preferable upper limit is 1.8%). It is preferable.
- Ni improves the Charpy impact absorption energy at a low temperature by lowering the brittle fracture surface transition temperature.
- it is preferable to contain 1.0% or more. However, if the content exceeds 2.0%, the amount of martensite generated increases and the strength increases, thereby reducing Charpy impact absorption energy.
- Mo 0.05 to 1.5%
- Mo is an element necessary for improving the strength of the weld metal, and in order to exert such effects, it is necessary to contain 0.05% or more.
- it is 0.10% or more, more preferably 0.2% or more.
- the content exceeds 1.5%, the hydrogen embrittlement susceptibility increases due to an excessive increase in strength.
- it is 1.0% or less, More preferably, it is 0.50% or less.
- Ti 0.040 to 0.150%
- Ti is an element that contributes to high-density dispersion of retained austenite particles by forming an oxide serving as a starting point of intragranular transformation and refining the structure. In order to exhibit such an effect, it is necessary to contain 0.040% or more. Preferably it is 0.050% or more, More preferably, it is 0.055% or more. However, if the content exceeds 0.150%, the hydrogen embrittlement susceptibility increases due to an excessive increase in strength. Preferably it is 0.12% or less, More preferably, it is 0.08% or less.
- N 0.015% or less (excluding 0%)
- N is an element inevitably mixed in, and is effective in improving the strength of the weld metal. However, if excessively contained, it causes a high hydrogen embrittlement susceptibility due to an excessive increase in strength. .
- the N content needs to be 0.015% or less. Preferably it is 0.010% or less, More preferably, it is 0.006% or less. In addition, it is difficult to make N into 0% industrially.
- O is an element that contributes to high-density dispersion of retained austenite particles by forming an oxide that serves as a starting point of intragranular transformation and by refining the structure. In order to exhibit such an effect, it is necessary to contain 0.030% or more. Preferably it is 0.035% or more, More preferably, it is 0.040% or more. However, when it is contained excessively exceeding 0.10%, Si oxide is formed, and the amount of retained austenite cannot be ensured due to a decrease in solute Si. Preferably it is 0.080% or less, More preferably, it is 0.060% or less.
- the contained elements specified in the present invention are as described above, and the balance is iron and inevitable impurities, and the elements (for example, P and S) brought in depending on the situation of raw materials, materials, manufacturing equipment, etc. as the inevitable impurities. Etc.) can be allowed to be mixed.
- impurities segregate at the grain boundaries to lower the grain boundary strength and promote low temperature cracking. Therefore, P: 0.02% or less (excluding 0%), S: 0.025% or less (0 % Is not included).
- Cr 2.0% or less (not including 0%), V: 0.60% or less (not including 0%), Nb: 0.15% or less (not including 0%), and Cu: 1.
- One or more selected from the group consisting of 0% or less (excluding 0%)] Cr, V, Nb, and Cu are elements necessary for improving the strength of the weld metal. However, if excessively contained, it causes an increase in hydrogen embrittlement sensitivity due to an excessive increase in strength.
- Cr is 2.0% or less (more preferably 1.5% or less, more preferably 1.0% or less)
- V is 0.60% or less (more preferably 0.50% or less, further preferably 0.40% or less)
- Nb 0.15% or less more preferably 0.10% or less, more preferably 0.08% or less
- Cu 1.0% or less (more preferably 0.5% or less). % Or less, more preferably 0.2% or less).
- the preferable minimum for exhibiting the said effect is 0.05% or more in Cr, 0.02% or more in V, 0.01% or more in Nb, or 0.05% or more in Cu.
- Al and Zr are both strong deoxidizing elements and have the effect of promoting the increase in retained austenite due to the increase in solid solution Si.
- Al and Zr are both strong deoxidizing elements and have the effect of promoting the increase in retained austenite due to the increase in solid solution Si.
- the intragranular transformation at the oxide origin is reduced and the structure becomes coarse. It causes high hydrogen embrittlement susceptibility. Therefore, it is preferable to suppress the content of Al to 0.020% or less (more preferably 0.018% or less) and Zr to 0.10% or less (more preferably 0.06% or less).
- the preferable minimum for exhibiting the said effect is 0.010% or more of both Al or Zr.
- B is an element that improves the strength by suppressing the formation of ferrite from the prior austenite grain boundaries. However, if excessively contained, the strength is excessively increased and the hydrogen embrittlement susceptibility is increased. For these reasons, B is preferably suppressed to 0.0050% or less (more preferably 0.0030% or less). In addition, the preferable minimum for exhibiting the said effect is 0.0010% or more.
- the wire component and the welding conditions are not particularly limited, but in order to realize the prescribed mode, A preferred range exists.
- a preferable wire component satisfies, for example, all of the following requirements. That is, for the total wire mass that combines the outer shell made of steel and the flux, (A) Total Si present in the form of metals, oxides, etc. is 0.35-2.5% (B) Si present in a form other than oxide is 0.25% or more. (C) Si present as oxide is 0.25% or less (D) 2.5 to 4.5% of total Ti present in the form of metals, oxides, etc.
- the ratio [(Mn + Ti) / Si] of the total amount of Si and the amount of (Mn + Ti) existing in the form satisfies the relationship of the following formula (4).
- the other components need not be particularly limited, but needless to say, they must be adjusted so as to satisfy the prescribed weld metal component range. (Mn + Ti) / Si> 10.0 (4)
- the above-mentioned requirements [(a) to (i)] are a control range for securing a solid solution Si amount effective for increasing the retained austenite amount. That is, as Si addition form, when Si existing in a form other than oxide is less than 0.25%, or when Si existing as oxide exceeds 0.25%, the total amount of Si is further 0.35. When the ratio is less than 1% [when the requirements (a) to (c) are not satisfied], the necessary amount of dissolved Si cannot be secured.
- the Si amount (total Si amount) and the Ti amount be large. However, if the amount exceeds 2.5% and 4.5%, respectively, the concentration in the weld metal Will exceed the specified upper limit.
- the above requirement (i) is for ensuring the number density of retained austenite particles. That is, in bainite, which is a main structure of the weld metal, retained austenite is generated between bainite laths. Therefore, in order to increase the number density of retained austenite particles, it is necessary to refine the base bainite structure.
- a Ti—Mn oxide is formed, and the bainite structure is refined by intragranular transformation starting from this oxide. Further, when the ratio is more than 10.0, the oxide is dispersed at a high density, and further refinement of the structure is achieved, leading to improvement in resistance to hydrogen embrittlement resistance.
- the welding conditions for forming the weld metal it is preferable to use a mixed gas comprising a heat input of 2.5 kJ / mm or less, 20% (volume%) CO 2 as the shielding gas, and the balance of Ar. .
- a mixed gas comprising a heat input of 2.5 kJ / mm or less, 20% (volume%) CO 2 as the shielding gas, and the balance of Ar.
- the composition of the shielding gas is intended to control the oxide form to achieve the refinement of the structure.
- the flux-cored wire is used for welding, but the flux filling rate of the wire used is usually about 10 to 20%.
- Example 1 Using a flux-cored wire (welding material) having the chemical composition shown in Tables 1 and 2 below with a wire diameter of 1.2 mm and a flux filling ratio of 13.5%, a weld metal was prepared according to the following procedures, and various performances ( Tensile strength, hydrogen embrittlement sensitivity) were evaluated. In Tables 1 and 2, the column indicated by “-” indicates no addition (not contained).
- a round bar specimen having a diameter of 5 mm was collected from the final pass of the produced weld metal (the collection position is shown in FIG. 2: corresponding to the original part), and a thermal cycle simulating a reheating cycle was applied.
- a thermal cycle (relationship between time and temperature) simulating the reheat cycle at this time is shown in FIG. Moreover, it shows in following Tables 3 and 4 with the welding material using the chemical component composition of each produced weld metal, and heat input conditions. In Tables 3 and 4, the column indicated by “ ⁇ ” indicates the amount of impurities (less than the impurity level).
- test piece for measuring hydrogen storage amount From the heat-treated test piece, a test piece for tensile test and a test piece for measuring hydrogen storage amount (test piece for measuring hydrogen storage amount) were collected.
- the shape of the tensile test piece is shown in FIG. 4, and the shape of the hydrogen storage amount measurement test piece is shown in FIG. Using these test pieces, the hydrogen embrittlement sensitivity was evaluated by the following method.
- Aqueous solution (0.5 mol / L or 2.5 mol / L H 2 SO 4 ) + (1 g / L-KSCN), (30 g / L-NaCl) + (1 g / L-KSCN)
- Current density 0.1 A / dm 2 , 1.0 A / dm 2 , 5.0 A / dm 2
- Charge time 24 hours
- the amount of diffusible hydrogen is determined by using a temperature-programmed desorption analyzer (manufactured by Nidec Anelva) with a built-in quadrupole mass spectrometer, did.
- Plate thickness 20mm V-shaped grooved SM490A steel plate, weld metal produced under the following welding conditions (welding materials shown in Tables 1 and 2), compliant with JIS-Z2202 Tensile test specimens were collected, subjected to a tensile test, and those having a tensile strength exceeding 780 MPa were regarded as acceptable. (Welding conditions) Shielding gas: 20% by volume CO 2 -80% by volume Ar mixed gas Current-Voltage-Welding speed: 270A-29V-4.5mm / sec Heat input: 1.74kJ / mm Preheating-pass temperature: 105-150 ° C Lamination method: 8 layers, 17 passes
- the number density of oxide particles containing 20% by mass or more of Ti and having an equivalent circle diameter of 0.15 to 1.0 ⁇ m the number density of residual austenite particles, and the total volume fraction of residual austenite particles, It measured by the following method.
- the analysis value of Ti (% by mass) is included in the oxide particles by standardizing the analysis value (% by mass) of Si, S, Ti, Mn, Al, Zr, and Mg.
- No. 30 to 54 are examples that do not satisfy any of the requirements defined in the present invention, and at least one of the properties of tensile strength and hydrogen embrittlement resistance is deteriorated.
- No. No. 30 is an example in which the heat input conditions during welding are not appropriate, the total volume fraction of residual austenite particles is low, and the hydrogen embrittlement susceptibility is high (the hydrogen embrittlement susceptibility is deteriorated). ).
- No. No. 31 is an example in which the Si content of the weld metal is excessive. The tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. No. 32 has a low total volume fraction of residual austenite particles (insufficient Si content in the welding material) and high hydrogen embrittlement susceptibility.
- No. No. 33 is an example in which the Ti content of the weld metal is insufficient, the number density of residual austenite particles is low, and the hydrogen embrittlement sensitivity is high.
- No. No. 34 is an example in which the Ti content of the weld metal is excessive. The tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. 35 is an example in which the Mn content of the weld metal is insufficient, the tensile strength is low, and the total volume fraction of residual austenite particles is low (the Al content in the welding material is insufficient), Hydrogen embrittlement sensitivity is high.
- No. 36 is an example in which the Ni content of the weld metal is insufficient, the tensile strength is low, and the total volume fraction of residual austenite particles is low (the Zr content in the welding material is insufficient), Hydrogen embrittlement sensitivity is high.
- No. No. 37 has a low total volume fraction of residual austenite particles (insufficient Mg content in the welding material) and high hydrogen embrittlement sensitivity.
- No. No. 38 has a low total volume fraction of residual austenite particles (insufficient metal Si content in the welding material) and high hydrogen embrittlement sensitivity.
- No. In No. 39 the total volume fraction of residual austenite particles is low (the amount of SiO 2 in the welding material is excessive), and the hydrogen embrittlement sensitivity is high.
- No. 40 the total volume fraction of residual austenite particles is low (the A value of the welding material is insufficient), and the hydrogen embrittlement sensitivity is high.
- No. No. 41 is an example in which the C content of the weld metal is insufficient, the tensile strength is low, the number density and total volume fraction of residual austenite particles are low, and the hydrogen embrittlement susceptibility is high.
- No. No. 42 is an example in which the C content of the weld metal is excessive. The tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. 43 is an example in which the Si content (total Si content) of the weld metal is insufficient (Mn content is also excessive), the tensile strength increases excessively, and the number density of residual austenite particles And the total volume fraction is low, and hydrogen embrittlement sensitivity is high.
- No. No. 44 is an example in which the Ni content of the weld metal is excessive, and the tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. 45 is an example in which the V content of the weld metal is excessive, the tensile strength is excessively increased, and the hydrogen embrittlement sensitivity is increased.
- No. No. 46 is an example in which the Nb content of the weld metal is excessive, the tensile strength is excessively increased, and the hydrogen embrittlement sensitivity is increased.
- No. No. 47 is an example in which the contents of N, O and Zr in the weld metal are excessive, and the tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. 48 is an example in which the Mo content of the weld metal is insufficient, and the tensile strength is low.
- No. No. 49 is an example in which the Mo content of the weld metal is excessive, and the tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. 50 is an example in which the O content of the weld metal is insufficient (Al content is also increased), the number density of residual austenite particles is low, and the hydrogen embrittlement susceptibility is high.
- No. No. 51 is an example in which the Ti content of the weld metal is excessive. The tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- No. No. 52 is an example in which the Cr content of the weld metal is excessive, the tensile strength is excessively increased, and the hydrogen embrittlement sensitivity is increased.
- No. 53 is an example in which the Cu content of the weld metal is excessive, the tensile strength is excessively increased, and the hydrogen embrittlement sensitivity is increased.
- No. No. 54 is an example in which the B content of the weld metal is excessive. The tensile strength is excessively increased and the hydrogen embrittlement sensitivity is increased.
- Example 2 Wire diameter: 1.2 mm, flux filling ratio: 13.5%, and flux-cored wires (welding materials) having the chemical composition shown in Table 7 below were used (Nos. 2, 4, 15, 16, 21, 24 are tables) 1) and a weld metal was prepared in the same procedure as in Example 1 (heat input condition was A), and various performances (tensile strength, hydrogen embrittlement sensitivity) were evaluated. In Table 7, the column indicated by “-” indicates no addition (not contained).
- a round bar test piece was collected in the same manner as in Example 1 (the collection position corresponds to the above-mentioned Fig. 2: original part), and a thermal cycle simulating a reheat cycle was given (Fig. 3). Moreover, it shows in following Table 8 with the welding material using the chemical component composition of each produced weld metal, and heat input conditions. In Table 8, the column indicated by “ ⁇ ” indicates the amount of impurities (less than the impurity level).
- the produced weld metal was measured for hydrogen embrittlement susceptibility, tensile strength, residual austenite number density and volume fraction, and oxide particle number density in the same manner as in Example 1. Toughness was measured.
- No. 55 has a Ni content outside the preferred range (1.0 to 2.0%).
- No. 56 has a Ni content outside the preferred range and an ⁇ value of less than 3.2.
- No. 57 has a Si content and a Ni content outside the preferred ranges.
- No. 60 has a Si content outside the preferable range (0.10 to 0.5%), and the low-temperature toughness is deteriorated in all cases.
- No. In 58 and 59 the ⁇ value defined by the formula (1) is less than 3.2, and the low temperature toughness is deteriorated.
- No. Nos. 61-69 have high strength and excellent resistance to hydrogen embrittlement as well as Si content and Ni content because the number density and total volume fraction of residual austenite particles are appropriately controlled together with the chemical composition.
- the amount is within a preferable range, and the ⁇ value defined by the formula (1) satisfies 3.2 or more, which indicates that good low temperature toughness is achieved.
- the weld metal of the present invention is used in various welded structures and can be applied to offshore structures.
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Abstract
Description
C:0.02~0.12%(「質量%」の意味。化学成分組成について、以下同じ)、Si:0.10~2.0%、Mn:0.90~2.5%、Ni:0.20~3.5%、Mo:0.05~1.5%、Ti:0.040~0.150%、N:0.015%以下(0%を含まない)およびO:0.030~0.10%を夫々含有し、残部が鉄および不可避的不純物からなり、
残留オーステナイト粒子が2500個/mm2以上存在すると共に、残留オーステナイト粒子の合計体積分率が4.0%以上である点に要旨を有するものである。尚、個数密度の測定に際し対象となる残留オーステナイト粒子の大きさは、測定限界以上(円相当直径で0.15μmを超えるもの)のものである。
α値=[Mn]+[Ni]+(2×[Mo])+(16×[Ti])-(12×[O])…(1)
但し、[Mn]、[Ni]、[Mo]、[Ti]および[O]は、夫々Mn、Ni、Mo、TiおよびOの含有量(質量%)を示す。
α値=[Mn]+[Ni]+(2×[Mo])+(16×[Ti])-(12×[O])…(1)
但し、[Mn]、[Ni]、[Mo]、[Ti]および[O]は、夫々Mn、Ni、Mo、TiおよびOの含有量(質量%)を示す。
Cは、溶接金属の強度を確保するために欠くことのできない元素であり、こうした効果を発揮させるには、0.02%以上含有させる必要がある。好ましくは0.04%以上であり、より好ましくは0.06%以上である。しかしながら、C含有量が0.12%を超えると、強度が過大に上昇して水素脆化感受性が高くなる(耐水素脆化感受性が劣化する)。尚、C含有量の好ましい上限は、0.10%であり、より好ましくは0.08%以下である。
Siは、固溶状態で存在することで炭化物形成を遅らせ、残留オーステナイトを安定化する作用を有する。Si含有量が0.10%未満であると、残留オーステナイトが確保できない。好ましくは0.25%以上、より好ましくは0.28%以上含有させるのがよい。しかしながら、Si含有量が過剰になると、強度の過大な上昇による水素脆化感受性が高くなるので、2.0%以下に抑える必要がある。好ましくは1.5%以下であり、より好ましくは0.5%以下に抑えるのが良い。特に、溶接金属の低温靭性を良好にするためには、Si含有量は0.5%以下(更に好ましくは0.4%以下)とすることが好ましい。即ち、Si含有量が0.5%を超えると、硬質な島状マルテンサイトが形成され、これが破壊の起点となることで、低温靭性が劣化しやすくなる。
Mnは、溶接金属の強度を確保する上で必要な元素であり、こうした効果を発揮させるには、0.90%以上含有させる必要がある。好ましくは1.2%以上、より好ましくは1.5%以上である。しかしながら、2.5%を超えて過剰に含有させると、強度の過大な上昇による水素脆化感受性が高くなる原因となる。好ましくは2.2%以下であり、より好ましくは2.0%以下である。
Niは、溶接金属の強度を確保する上で必要な元素であり、こうした効果を発揮させるには、0.20%以上含有させる必要がある。好ましくは0.5%以上、より好ましくは1.0%以上である。しかしながら、3.5%を超えて過剰に含有させると、強度の過大な上昇による水素脆化感受性が高くなる原因となる。好ましくは3.0%以下であり、より好ましくは2.8%以下である。特に、溶接金属の低温靭性を良好にするためには、Ni含有量は1.0%以上2.0%以下(更に好ましい下限は1.1%、更に好ましい上限は1.8%)とすることが好ましい。Niは、脆性破面遷移温度を低温化させることで、低温でのシャルピー衝撃吸収エネルギーを向上させる。こうした効果を発揮させるには、1.0%以上含有させることが好ましい。しかしながら、2.0%を超えて含有させると、マルテンサイト生成量が増え、強度が上昇することで、シャルピー衝撃吸収エネルギーが低下する。
Moは、溶接金属の強度を向上する上で必要な元素であり、こうした効果を発揮させるには、0.05%以上含有させる必要がある。好ましくは0.10%以上、より好ましくは0.2%以上である。しかしながら、1.5%を超えて過剰に含有させると、強度の過大な上昇による水素脆化感受性が高くなる原因となる。好ましくは1.0%以下であり、より好ましくは0.50%以下である。
Tiは、粒内変態の起点となる酸化物を形成し、組織を微細化することで残留オーステナイト粒子の高密度分散に寄与する元素である。こうした効果を発揮させるには、0.040%以上含有させる必要がある。好ましくは0.050%以上、より好ましくは0.055%以上である。しかしながら、0.150%を超えて過剰に含有させると、強度の過大な上昇による水素脆化感受性が高くなる原因となる。好ましくは0.12%以下であり、より好ましくは0.08%以下である。
Nは、不可避的に混入してくる元素であり、溶接金属の強度を向上する上で有効であるが、過剰に含有させると、強度の過大な上昇による水素脆化感受性が高くなる原因となる。こうしたことから、N含有量は0.015%以下とする必要がある。好ましくは0.010%以下であり、より好ましくは0.006%以下である。尚、Nは工業的に0%とすることは困難である。
Oは、粒内変態の起点となる酸化物を形成し、組織を微細化することで残留オーステナイト粒子の高密度分散に寄与する元素である。こうした効果を発揮させるには、0.030%以上含有させる必要がある。好ましくは0.035%以上、より好ましくは0.040%以上である。しかしながら、0.10%を超えて過剰に含有させると、Si酸化物が形成されるようになり、固溶Siが減少することで残留オーステナイト量が確保できなくなる。好ましくは0.080%以下であり、より好ましくは0.060%以下である。
Cr,V,NbおよびCuは、溶接金属の強度を向上する上で必要な元素であるが、過剰に含有させると、強度の過大な上昇により水素脆化感受性が高くなる原因となる。こうしたことから、Crで2.0%以下(より好ましくは1.5%以下、更に好ましくは1.0%以下)、Vで0.60%以下(より好ましくは0.50%以下、更に好ましくは0.40%以下)、Nbで0.15%以下(より好ましくは0.10%以下、更に好ましくは0.08%以下)、またはCuで1.0%以下(より好ましくは0.5%以下、更に好ましくは0.2%以下)に、夫々抑制することが好ましい。尚、上記効果を発揮させるための好ましい下限は、Crで0.05%以上、Vで0.02%以上、Nbで0.01%以上、またはCuで0.05%以上である。
AlとZrは、いずれも強脱酸元素であり、固溶Si増加による残留オーステナイト増加を促進する作用があるが、過剰に含有させると、酸化物起点の粒内変態を減少させ、組織粗大化による水素脆化感受性が高くなる原因となる。こうしたことから、Alで0.020%以下(より好ましくは0.018%以下)、Zrで0.10%以下(より好ましくは0.06%以下)に、夫々抑制することが好ましい。尚、上記効果を発揮させるための好ましい下限は、AlまたはZrのいずれも0.010%以上である。
Bは、旧オーステナイト粒界からのフェライト生成を抑制することで、強度を向上させる元素であるが、過剰に含有させると、強度を過大に上昇させ、水素脆化感受性が高くなる原因となる。こうしたことから、Bは0.0050%以下(より好ましくは0.0030%以下)に、抑制することが好ましい。尚、上記効果を発揮させるための好ましい下限は、0.0010%以上である。
(a)金属、酸化物その他の形態で存在する全Siが0.35~2.5%
(b)酸化物以外の形態で存在するSiが0.25%以上
(c)酸化物として存在するSiが0.25%以下
(d)金属、酸化物その他の形態で存在する全Tiが2.5~4.5%
(e)金属、酸化物その他の形態で存在する全Alが0.10%以上
(f)金属、酸化物その他の形態で存在する全Zrが0.035%以上
(g)金属として存在するMgが0.4%以上
(h)金属、酸化物その他の形態で存在する全Si,Ti,Al,ZrおよびMgの各量から、下記(2)式に基づいて求められるA値が0.30以上
A値=Si-[Si/(Ti+2Al+2Zr+3.5Mg)] …(2)
(i)金属、酸化物その他の形態で存在する全Si量と(Mn+Ti)量の比[(Mn+Ti)/Si]が下記(3)式の関係を満足すること
(Mn+Ti)/Si>4.0 …(3)
(Mn+Ti)/Si>10.0 …(4)
ワイヤ径:1.2mm、フラックス充填率:13.5%で下記表1、2に示す化学成分組成のフラックス入りワイヤ(溶接材料)を用い、溶接金属を下記の手順で作成し、各種性能(引張強度、水素脆化感受性)を評価した。尚、表1、2中、「-」で示した欄は、無添加(含有せず)であることを示している。
SM490A鋼板を、図1に示す開先形状に加工し、下記の溶接条件でガスシールドアーク溶接を実施し、溶接金属を作製した。
シールドガス:20体積%CO2-80体積%Ar混合ガス
電流-電圧-溶接速度:270A-29V-3.0~4.5mm/秒
入熱条件:
(A)1.74kJ/mm(270A-29V-4.5mm/秒)
(B)2.37kJ/mm(270A-29V-3.3mm/秒)
(C)2.61kJ/mm(270A-29V-3.0mm/秒)
予熱-パス間温度:105~150℃
積層法:3層13パス
上記で得られた水素吸蔵量測定用試験片を用い、拡散性水素量=1.5~3.0ppmとなるような水素チャージ条件を選定した。このとき採用したチャージ条件は、下記の通りである。
電流密度:0.1A/dm2、1.0A/dm2、5.0A/dm2
チャージ時間:24時間
水溶液:(350g/L-ZnSO4・7H2O)+(20.6g/L-H2SO4(97%))+(60g/L-Na2SO4)
浴温:60℃
電流密度:50A/dm2
めっき時間:3分
S=(1-Eh/E0)×100(%)…(5)
板厚:20mmのSM490A鋼板に、20°V字開先を施し、下記の溶接条件で作製した溶接金属について(溶接材料については、表1、2に示したもの)、JIS-Z2202に準拠した引張り試験片を採取し、引張り試験を行い、引張り強度にして780MPaを超えるものを合格とした。
(溶接条件)
シールドガス:20体積%CO2-80体積%Ar混合ガス
電流-電圧-溶接速度:270A-29V-4.5mm/秒
入熱量:1.74kJ/mm
予熱-パス間温度:105~150℃
積層法:8層17パス
SSRT試験用に作製した溶接金属(前記「溶接金属の作製」の欄)の最終パスより、直径:5mmの丸棒試験片を採取し、輪切り断面を鏡面研磨した後、光学顕微鏡にて1000倍の画像を2視野撮影した。画像解析ソフト(「Image-Pro Plus」 Media Cybernetics社製)によって、円相当直径:0.15~1.0μmの酸化物粒子を選定すると共に、撮影した酸化物中央部の組成をSEM-EDS(Energy-dispersive X-ray spectroscopy)にて分析した。検出された元素のうち、Tiの分析値(質量%)をSi,S,Ti,Mn,Al,Zr,Mgの分析値(質量%)の合計で規格化することで、酸化物粒子に含まれるTi濃度(質量%)を算出し、20質量%以上のTiを含有する酸化物粒子であって、円相当直径が0.15~1.0μmのものの個数密度を算出した。
酸化物粒子の個数密度を測定したサンプルを、レペラ試薬で腐食させ、光学顕微鏡にて1000倍の画像を2視野撮影した。残留オーステナイトの白い腐食コントラストを、画像解析ソフト(上記と同じ)により解析し、円相当直径にして0.15μmを超える残留オーステナイト粒子の個数密度を算出した。
上記サンプル表面を電解研磨し、リガク社製の二次元微小部X線回折装置(「RINT-RAPIDII」)にてX線回折測定を実施した。フェライト相の(110)、(200)、(211)、(220)の各格子面のピーク、および残留オーステナイト相の(111)、(200)、(220)、(311)の各格子面のピークについて、各ピークの積分強度比に基づき、残留オーステナイト相の体積分率を算出し、各組み合わせの平均値を求めた。
ワイヤ径:1.2mm、フラックス充填率:13.5%で下記表7に示す化学成分組成のフラックス入りワイヤ(溶接材料)を用い(No.2、4、15、16、21、24は表1に示したものと同じ)、溶接金属を実施例1と同様の手順で作製し(入熱条件はA)、各種性能(引張り強度、水素脆化感受性)を評価した。尚、表7中、「-」で示した欄は、無添加(含有せず)であることを示している。
引張り強度測定用に作製した溶接金属の板厚中央部より、溶接線方向に垂直にシャルピー衝撃試験片(JIS Z 3111 4号試験Vノッチ試験片)を採取し、JIS Z 2242の要領で、-40℃での衝撃吸収エネルギーvEー40を測定した。このとき3回の測定の平均値が85Jを超えるものを低温靭性に優れると評価した。
本出願は、2011年2月2日出願の日本特許出願(特願2011-021153)及び2011年8月25日出願の日本特許出願(特願2011-184117)に基づくものであり、その内容はここに参照として取り込まれる。
Claims (6)
- フラックス入りワイヤを用い、ガスシールドアーク溶接によって形成される溶接金属であって、
C:0.02~0.12%(「質量%」の意味。化学成分組成について、以下同じ)、Si:0.10~2.0%、Mn:0.90~2.5%、Ni:0.20~3.5%、Mo:0.05~1.5%、Ti:0.040~0.150%、N:0.015%以下(0%を含まない)およびO:0.030~0.10%を夫々含有し、残部が鉄および不可避的不純物からなり、
残留オーステナイト粒子が2500個/mm2以上存在すると共に、残留オーステナイト粒子の合計体積分率が4.0%以上であることを特徴とする耐水素脆化感受性に優れた溶接金属。 - Si:0.10~0.5%およびNi:1.0~2.0%を夫々満足すると共に、下記(1)式で規定されるα値が3.2以上である請求項1に記載の溶接金属。
α値=[Mn]+[Ni]+(2×[Mo])+(16×[Ti])-(12×[O])…(1)
但し、[Mn]、[Ni]、[Mo]、[Ti]および[O]は、夫々Mn、Ni、Mo、TiおよびOの含有量(質量%)を示す。 - 20質量%以上のTiを含有する酸化物粒子で、円相当直径:0.15~1.0μmのものが5000個/mm2以上存在するものである請求項1または2に記載の溶接金属。
- 更に、Cr:2.0%以下(0%を含まない)、V:0.60%以下(0%を含まない)、Nb:0.15%以下(0%を含まない)およびCu:1.0%以下(0%を含まない)よりなる群から選ばれる1種以上を含有するものである請求項1~3のいずれかに記載の溶接金属。
- 更に、Al:0.020%以下(0%を含まない)および/またはZr:0.10%以下(0%を含まない)を含有するものである請求項1~4のいずれかに記載の溶接金属。
- 更に、B:0.0050%以下(0%を含まない)を含有するものである請求項1~5のいずれかに記載の溶接金属。
Priority Applications (7)
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RU2013140454/02A RU2535417C1 (ru) | 2011-02-02 | 2012-02-01 | Металл сварного шва с высокой устойчивостью к водородному охрупчиванию |
US13/982,761 US9718150B2 (en) | 2011-02-02 | 2012-02-01 | Weld metal excellent in hydrogen embrittlement resistance |
KR1020137020478A KR101484873B1 (ko) | 2011-02-02 | 2012-02-01 | 내수소 취화 감수성이 우수한 용접 금속 |
CA2822966A CA2822966C (en) | 2011-02-02 | 2012-02-01 | Weld metal excellent in hydrogen embrittlement resistance |
EP12741500.8A EP2671668A4 (en) | 2011-02-02 | 2012-02-01 | WELDING METAL WITH EXCELLENT RESISTANCE TO HYDROGEN INJURY |
CN201280007329.XA CN103338894B (zh) | 2011-02-02 | 2012-02-01 | 耐氢脆化敏感性优异的焊接金属 |
SG2013050513A SG191777A1 (en) | 2011-02-02 | 2012-02-01 | Weld metal excellent in hydrogen embrittlement resistance |
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JP2011184117A JP5607002B2 (ja) | 2011-02-02 | 2011-08-25 | 耐水素脆化感受性に優れた溶接金属 |
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WO2013129284A1 (ja) * | 2012-02-27 | 2013-09-06 | 株式会社神戸製鋼所 | 耐水素脆化感受性に優れた溶接金属 |
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JP7564428B2 (ja) | 2020-09-02 | 2024-10-09 | 日本製鉄株式会社 | 溶接金属及び溶接継手 |
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KR20130100014A (ko) | 2013-09-06 |
EP2671668A4 (en) | 2016-07-27 |
CN103338894B (zh) | 2016-08-10 |
JP2012176434A (ja) | 2012-09-13 |
CN103338894A (zh) | 2013-10-02 |
CA2822966A1 (en) | 2012-08-09 |
EP2671668A1 (en) | 2013-12-11 |
MY158424A (en) | 2016-10-14 |
CA2822966C (en) | 2016-01-26 |
US20130315777A1 (en) | 2013-11-28 |
US9718150B2 (en) | 2017-08-01 |
SG191777A1 (en) | 2013-08-30 |
JP5607002B2 (ja) | 2014-10-15 |
KR101484873B1 (ko) | 2015-01-20 |
RU2535417C1 (ru) | 2014-12-10 |
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