WO2014136601A1 - 溶接金属及びこれを備えた溶接構造体 - Google Patents
溶接金属及びこれを備えた溶接構造体 Download PDFInfo
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- WO2014136601A1 WO2014136601A1 PCT/JP2014/054345 JP2014054345W WO2014136601A1 WO 2014136601 A1 WO2014136601 A1 WO 2014136601A1 JP 2014054345 W JP2014054345 W JP 2014054345W WO 2014136601 A1 WO2014136601 A1 WO 2014136601A1
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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
- B23K35/22—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
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- 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
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- 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
- B23K35/362—Selection of compositions of fluxes
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/36—Selection of non-metallic compositions, e.g. coatings, fluxes; Selection of soldering or welding materials, conjoint with selection of non-metallic compositions, both selections being of interest
- B23K35/368—Selection of non-metallic compositions of core materials either alone or conjoint with selection of soldering or welding materials
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- 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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- 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
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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- 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 applied in a welded structure such as an offshore structure, and a welded structure including the weld metal, and in particular, a weld metal with improved strength and low-temperature toughness after stress relief annealing, and
- the present invention relates to a welded structure including such a weld metal.
- FCW Flux Cored Wire, depending on the case
- FCW Flux Cored Wire
- Patent Document 1 high strength and excellent low temperature toughness are ensured in the weld metal after SR annealing by controlling the amount and number density of carbides.
- this technology mainly assumes weld metal formed by applying submerged arc welding, and such submerged arc welding is limited to working postures and can be used for all posture welding that is unavoidable for large steel structures. There are some problems that cannot be handled.
- Patent Document 2 high strength and excellent low temperature toughness are ensured after SR annealing by finely controlling the size of carbides that tend to be coarse.
- the toughness evaluation temperature is somewhat high at ⁇ 30 ° C., and it cannot be said that the toughness at a lower temperature of ⁇ 40 ° C. is guaranteed.
- Patent Document 3 proposes a welding material that can ensure high strength and excellent low-temperature toughness after SR annealing by controlling the contents of C, Si, Mn, Mo, Ti, Ni, Al, and O. .
- the toughness evaluation temperature is somewhat high at ⁇ 29 ° C., and it cannot be said that the toughness at the lower temperature of ⁇ 40 ° C. is guaranteed.
- the welding method applied assumes TIG welding with low construction efficiency, and further improvement is desired from the viewpoint of construction cost.
- Patent Document 4 in a flux-cored wire capable of improving the efficiency of welding, it is high after SR annealing by adding an appropriate amount of Cr, Mo, Cu, Ti, B, etc. to the wire and controlling the composition of the slag agent.
- a welding material that can ensure strength and excellent low-temperature toughness is disclosed.
- the toughness evaluation temperature is somewhat high at ⁇ 30 ° C., and it cannot be said that the toughness at ⁇ 40 ° C., which is a lower temperature, is guaranteed.
- Patent Document 5 proposes a welding material capable of ensuring high strength and excellent low-temperature toughness after SR annealing by controlling the form of grain boundary carbides.
- the toughness evaluation temperature is slightly high at ⁇ 30 ° C., and low temperature toughness at a lower temperature of ⁇ 40 ° C. cannot be guaranteed.
- the present invention has been made in view of the above circumstances, and the purpose thereof is, together with high strength after SR annealing, even when gas shielded arc welding using a flux cored wire excellent in work efficiency is applied. It is an object of the present invention to provide a weld metal that exhibits excellent low temperature toughness at a lower temperature, and a welded structure including such a weld metal.
- the weld metal according to the present invention capable of solving the above problems is C: 0.02 to 0.10% (meaning “mass%”, the same applies hereinafter), Si: 0.10 to 0.60%, Mn: 0.90 to 2.5%, Ni: 0.20 to 2.00%, Cr: 0.05 to 1.0%, Mo: 0.10 to 1.50%, Ti: 0.040 to 0.15%, B: 0.0010 to 0.0050%, O: 0.030 to 0.100%, N: 0.015% or less (excluding 0%), respectively, the balance being iron and Among the carbides that are unavoidable impurities and exist at the grain boundaries of the weld metal, the gist is that the average equivalent circle diameter of carbides having an equivalent circle diameter of 0.40 ⁇ m or more is 0.75 ⁇ m or less.
- the “equivalent circle diameter” refers to the size of carbide particles recognized on the observation surface of a microscope (for example, Transmission Electron Microscope (TEM)) so that the areas thereof are equal. This is the diameter of the circle assumed.
- TEM Transmission Electron Microscope
- the weld metal of the present invention as other elements, at least one of (a) Cu: 1.0% or less (not including 0%) and V: 0.40% or less (not including 0%) is used. (B) Al: 0.030% or less (not including 0%) is also preferably included, and the properties of the weld metal are further improved depending on the type of element to be included.
- the present invention also includes a welded structure including the above weld metal.
- the average equivalent circle diameter of carbide of a predetermined size existing in the weld metal is specified together with the chemical composition, it has sufficient strength even after SR annealing, even at low temperatures. Excellent weld metal can be realized.
- the present inventors have studied from various angles in order to realize a weld metal that exhibits high strength and excellent low-temperature toughness after SR annealing.
- the chemical component composition of the weld metal is controlled while adding Mo which has the effect of suppressing coarsening and annealing softening of grain boundary carbides by fine precipitation within the grains, and at the time of welding the grain boundaries of the weld metal.
- the inventors have found that the above-mentioned characteristics can be combined by defining the average equivalent circle diameter of carbide of a predetermined size generated above (this carbide may be referred to as “grain boundary carbide”), and the present invention has been completed. .
- the chemical component composition of the weld metal is appropriately controlled while setting the Mo content to 0.10% or more, and the average equivalent circle diameter of grain boundary carbides having a circle equivalent diameter of 0.40 ⁇ m or more is 0.
- the thickness is not more than .75 ⁇ m, both high strength and low temperature toughness can be achieved.
- control of grain boundary carbides is extremely important.
- the larger the size of the carbide generated in the SR annealing the lower the toughness, but the grain boundary carbide generated at the grain boundary tends to be coarser than the carbide in the grain.
- the prior austenite grain boundaries become brittle by annealing (tempering embrittlement)
- cracks tend to preferentially progress in the Charpy test for evaluating toughness.
- the toughness value of the weld metal significantly deteriorates during SR annealing. Therefore, in order to ensure excellent low temperature toughness after SR annealing, it is important to suppress temper embrittlement and to keep the grain boundary carbide fine.
- the average equivalent circle diameter of carbides having a circle equivalent diameter of 0.40 ⁇ m or more is defined as 0.75 ⁇ m or less.
- the average equivalent circle diameter is preferably 0.70 ⁇ m or less, and more preferably 0.65 ⁇ m or less.
- the grain boundary carbide size is remarkably refined, and the average equivalent circle diameter of the grain boundary carbide cannot be evaluated even by the grain boundary carbide evaluation method described later.
- the average equivalent circle diameter of the above carbides is included in 0.75 ⁇ m or less ”.
- C (C: 0.02-0.10%) C is an element necessary for ensuring the strength of the weld metal after SR annealing.
- the preferable lower limit of the C content is 0.03% or more (more preferably 0.04% or more), and the preferable upper limit is 0.08% or less (more preferably 0.07% or less).
- Si 0.10 to 0.60%
- Si is an element necessary for ensuring the strength of the weld metal after SR annealing.
- Si content is less than 0.10%, a predetermined strength cannot be obtained.
- the Si content is excessive, temper embrittlement during SR annealing is promoted and the toughness is reduced, so the content is made 0.60% or less.
- the preferable lower limit of the Si content is 0.12% or more (more preferably 0.15% or more), and the preferable upper limit is 0.50% or less (more preferably 0.45% or less).
- Mn is an element effective in forming an oxide that is a starting point for generating a microstructure during welding and improving the strength and toughness of the weld metal.
- the Mn content needs to be 0.90% or more.
- the minimum with preferable Mn content is 1.1% or more (more preferably 1.3% or more), and a preferable upper limit is 2.2% or less (more preferably 2.0% or less).
- Ni is an element effective for improving the toughness of the weld metal.
- the Ni content needs to be 0.20% or more.
- the minimum with preferable Ni content is 0.4% or more (more preferably 0.6% or more), and a preferable upper limit is 1.80% or less (more preferably 1.60% or less).
- Cr 0.05-1.0% Cr is an element having an effect of refining grain boundary carbides during SR annealing. In order to exert such effects, the Cr content needs to be 0.05% or more. However, if the Cr content is excessive, the grain boundary carbides are coarsened to reduce the toughness, so it is necessary to make the content 1.0% or less. In addition, the minimum with preferable Cr content is 0.20% or more (more preferably 0.30% or more), and a preferable upper limit is 0.80% or less (more preferably 0.70% or less).
- Mo 0.10 to 1.50%
- Mo is an important element for suppressing coarsening and annealing softening of grain boundary carbides.
- the Mo content needs to be 0.10% or more.
- the Mo content is excessive, the toughness is reduced due to an excessive increase in strength during SR annealing, so it is necessary to make it 1.50% or less.
- the minimum with preferable Mo content is 0.20% or more (more preferably 0.30% or more), and a preferable upper limit is 1.2% or less (more preferably 1.0% or less).
- Ti 0.040-0.15%
- Ti is an element effective in forming an oxide that serves as a starting point for generating a microstructure during welding and improving the toughness of the weld metal.
- the Ti content needs to be 0.040% or more.
- the preferable lower limit of the Ti content is 0.050% or more (more preferably 0.055% or more), and the preferable upper limit is 0.110% or less (more preferably 0.090% or less).
- B is an element effective in suppressing the formation of grain boundary ferrite that adversely affects the strength and toughness of the weld metal.
- the B content needs to be 0.0010% or more.
- the preferable lower limit of the B content is 0.0012% or more (more preferably 0.0015% or more), and the preferable upper limit is 0.0045% or less (more preferably 0.0040% or less).
- O is an element useful for forming an oxide serving as a starting point for generating a microstructure during welding and improving the toughness of the weld metal.
- the O content needs to be 0.030% or more. However, if the O content is excessive and exceeds 0.100%, the oxide becomes coarse and the toughness is reduced.
- the preferable lower limit of the O content is 0.035% or more (more preferably 0.040% or more), and the preferable upper limit is 0.080% or less (more preferably 0.060% or less).
- N 0.015% or less (excluding 0%)
- N is an element inevitably contained in the weld metal, and it is industrially impossible to make its content 0%. However, if the N content is excessive, the toughness is adversely affected, so it is necessary to make it 0.015% or less.
- the upper limit with preferable N content is 0.010% or less (more preferably 0.008% or less).
- the contained elements specified in the present invention are as described above, and the balance is iron and unavoidable impurities, and the elements (for example, P, S) brought in as raw materials, materials, production facilities, etc. as the unavoidable impurities. , Sn, etc.) can be permitted.
- the inevitable impurities particularly P is an element that remarkably promotes temper embrittlement during SR annealing, and therefore it is preferably suppressed to at least 0.010% or less.
- the weld metal of the present invention as other elements, at least one of (a) Cu: 1.0% or less (not including 0%) and V: 0.40% or less (not including 0%) is used. (B) Al: 0.030% or less (not including 0%) is preferably contained, and the properties of the weld metal are further improved depending on the type of element to be contained. The reason for setting the range when these elements are contained is as follows.
- Cu 1.0% or less (not including 0%) and V: 0.40% or less (not including 0%)
- Cu is an element useful for ensuring the strength of the weld metal.
- the content is preferably 1.0% or less (more preferably 0.80% or less).
- the content shall be 0.05% or more (more preferably 0.10% or more).
- V is an element effective for forming fine carbides during SR annealing to improve the strength, but if excessively contained, the strength increases excessively and causes a decrease in toughness.
- the content when V is contained, the content is preferably 0.40% or less (more preferably 0.30% or less). In order to effectively exert the effect of containing V, the content is preferably 0.05% or more (more preferably 0.10% or more).
- Al 0.030% or less (excluding 0%)
- Al is an element that is useful for improving the strength and toughness of the weld metal by forming an oxide that serves as a starting point for the formation of a microstructure during welding. When exceeding, the coarsening of an oxide will be caused and toughness will be reduced instead.
- the minimum with preferable Al content is 0.005% or more (more preferably 0.010% or more), and a preferable upper limit is 0.025% or less (more preferably 0.020% or less).
- the welding method for obtaining the weld metal of the present invention assumes gas shielded arc welding using a flux cored wire (FCW), and by applying such arc welding method, work efficiency at the time of welding is also improved. Will improve.
- FCW flux cored wire
- the welding material component is naturally constrained by the required welding metal component, and in order to obtain a predetermined carbide form, the welding conditions and the welding material component must be appropriately controlled.
- the preferred welding conditions in gas shielded arc welding using a flux cored wire are a welding heat input of 2.5 kJ / mm or less and a preheating-pass temperature during welding of 180 ° C. or less.
- the welding material ratio of metal Si amount and the amount of SiO 2 in (flux cored wire) used (metal Si / SiO 2) is preferably 0.90 or more.
- the welding heat input is preferably as small as possible, preferably 2.0 kJ / mm or less, more preferably 1.6 kJ / mm or less.
- the lower limit of the welding heat input is preferably about 0.7 kJ / mm or more in consideration of the construction efficiency during welding.
- the preheating-pass temperature is more preferably 160 ° C. or less.
- the interpass temperature is preferably 100 ° C. or higher, more preferably 120 ° C. or higher.
- the ratio of metal Si amount to SiO 2 amount (metal Si / SiO 2 ) in the welding material (flux-cored wire) is less than 0.90, solid solution Si is insufficient, resulting in destabilization of carbides,
- the ratio (metal Si / SiO 2 ) is more preferably 0.93 or more, and further preferably 1.00 or more.
- the upper limit of the value of this ratio (metal Si / SiO 2 ) is generally preferably 3.0 or less (more preferably 2.5 or less) from the viewpoint of workability during welding.
- the SR annealing conditions may be performed in accordance with conventional conditions, but from the viewpoint of controlling grain boundary carbides, the conditions are preferably set as follows.
- the SR annealing temperature is preferably 680 ° C. or less, more preferably 650 ° C. or less.
- the lower limit of the SR annealing temperature is preferably 580 ° C. or higher in consideration of the stress removal effect during welding.
- the SR annealing time is preferably 12 hours or less, more preferably 10 hours or less.
- the minimum of annealing time when the stress removal effect at the time of welding is considered, it is preferable that it is 2 hours or more.
- a weld metal having sufficient strength and exhibiting excellent low-temperature toughness can be obtained, and a welded structure including such a weld metal can be realized.
- a flux-cored wire having a wire diameter of ⁇ 1.2 mm and a flux filling rate of 15.5% was prepared (chemical composition is shown in Tables 1 and 2 below), and the characteristics were evaluated as follows.
- SM490A steel plate (base material) is processed into a groove shape shown in FIG. 1, a weld metal is produced by gas shielded arc welding under each welding condition described later, heat treatment (SR annealing) is performed, and various properties are evaluated. did.
- FIG. 2A, B an area indicated by a broken-line circle (indicated by “B” in the figure) is a virtual representation of the size of a circle having a diameter of 0.40 ⁇ m (reference to the size of the target carbide). It is.
- a carbide having an equivalent circle diameter intersecting with the straight line Ai of 0.40 ⁇ m or more is selected (FIG. 2C), and an average equivalent circle diameter is calculated by image analysis.
- the straight line A1 shown in FIG. 2B is a straight line that intersects the carbides 1, 2, and 3.
- the straight line A2 is a straight line that intersects with the carbides 2, 3, and 4
- the straight line A3 is a straight line that intersects with the carbides 3, 4, and 5
- the straight line A4 is a straight line that intersects with the carbides 4, 5, and 6,
- the straight line A5 is the carbides 5, 8, and 9, a straight line A6 is a straight line intersecting with the carbides 8, 9, 10,
- the chemical composition of the various welding materials (flux-cored wires) used when forming the weld metal is shown in Tables 1 and 2 below (welding materials Nos. F1 to F51).
- the chemical composition of the formed weld metal is shown in Tables 3 and 4 below (Test Nos. 1 to 51) together with the welding conditions (welding material No., heat input conditions, preheating-pass temperature).
- the evaluation characteristic results (carbide average equivalent circle diameter, tensile strength (TS), low temperature toughness (vE- 40 ) of each weld metal are shown in the following Tables 5 and 6 together with the SR annealing conditions (SR temperature, SR time) ( (Test Nos.
- Test No. Nos. 1 to 31 are examples that satisfy the requirements defined in the present invention.
- a weld metal having sufficient strength (TS> 620 MPa) and excellent low temperature toughness (vE ⁇ 40 > 60 J) is obtained. I understand that.
- test no. 32 to 51 are examples that do not meet any of the requirements defined in the present invention. Either property is inferior.
- test No. In No. 32 the heat input is higher than the appropriate range (heat input is 2.6 kJ / mm), the average equivalent circle diameter of the grain boundary carbide is increased, the strength is insufficient, and the low temperature toughness (vE ⁇ 40 ). Has deteriorated.
- Test No. In No. 33 the preheating-pass temperature is higher than the appropriate range (the preheating-pass temperature is 190 ° C.), the average equivalent circle diameter of the grain boundary carbide is increased, the strength is insufficient, and the low temperature toughness (vE -40 ) has deteriorated.
- Test No. 34 uses a welding material having a ratio (metal Si / SiO 2 ) smaller than 0.90, and the average equivalent circle diameter of the grain boundary carbide is increased, and the low temperature toughness (vE ⁇ 40 ) is deteriorated. Yes. Test No. In 35 and 36, the SR annealing conditions (temperature, time) are outside the appropriate range, and the average equivalent circle diameter of the grain boundary carbide is large, and the low temperature toughness (vE- 40 ) is deteriorated.
- Test No. 41 the Si content of the weld metal is excessive due to the high content of metal Si in the welding material, and the low-temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. 42 the B content of the weld metal is excessive, and the low-temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. No. 43 has an excessive content of Al, which is a selective component, resulting in insufficient strength and low temperature toughness (vE ⁇ 40 ).
- Test No. 44 the B content of the weld metal is insufficient, the strength is insufficient, and the low temperature toughness (vE- 40 ) is deteriorated.
- Test No. 45 the Mo content of the weld metal is excessive, and the low temperature toughness (vE- 40 ) is deteriorated.
- Test No. 46 the Ni content of the weld metal is excessive, and the low temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. 47 the Ti content of the weld metal is insufficient, and the low-temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. In No. 48 the Ti content of the weld metal is excessive, and the low temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. 49 the O content of the weld metal is insufficient, the N content is excessive, and the low temperature toughness (vE- 40 ) is deteriorated.
- Test No. 50 the O content of the weld metal is excessive, the Cu content as a selective component is excessive, and the low temperature toughness (vE ⁇ 40 ) is deteriorated.
- Test No. In No. 51 the V content of the weld metal is excessive, and the refinement of carbide is achieved, but the low-temperature toughness (vE ⁇ 40 ) is deteriorated.
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Abstract
Description
Cは、SR焼鈍後における溶接金属の強度を確保する上で必要な元素である。C含有量が0.02%よりも少なくなると、所定の強度が得られない。しかしながら、C含有量が過剰になると、SR焼鈍時に粒界炭化物の粗大化を招くことで、靱性低下の原因となるので0.10%以下とする。C含有量の好ましい下限は0.03%以上(より好ましくは0.04%以上)であり、好ましい上限は0.08%以下(より好ましくは0.07%以下)である。
Siは、SR焼鈍後における溶接金属の強度を確保する上で必要な元素である。Si含有量が0.10%よりも少なくなると、所定の強度が得られない。しかしながら、Si含有量が過剰になると、SR焼鈍時の焼戻し脆化を助長し、靱性低下の原因となるので0.60%以下とする。Si含有量の好ましい下限は0.12%以上(より好ましくは0.15%以上)であり、好ましい上限は0.50%以下(より好ましくは0.45%以下)である。
Mnは、溶接時の微細組織生成の起点となる酸化物を形成し、溶接金属の強度、靱性を向上させる上で有効な元素である。こうした効果を発揮させるためには、Mnの含有量は0.90%以上とする必要がある。しかしながら、Mn含有量が過剰になると、SR焼鈍時の焼戻し脆化を助長し、靱性低下の原因となるので2.5%以下とする必要がある。尚、Mn含有量の好ましい下限は1.1%以上(より好ましくは1.3%以上)であり、好ましい上限は2.2%以下(より好ましくは2.0%以下)である。
Niは、溶接金属の靱性向上に有効な元素である。こうした効果を発揮させるためには、Niの含有量は0.20%以上とする必要がある。しかしながら、Ni含有量が過剰になると、シャルピー試験における上部棚エネルギーを低下させるため、SR焼鈍後において所定の靱性が得られなくなるので、Niの含有量は2.00%以下とする必要がある。尚、Ni含有量の好ましい下限は0.4%以上(より好ましくは0.6%以上)であり、好ましい上限は1.80%以下(より好ましくは1.60%以下)である。
Crは、SR焼鈍時の粒界炭化物を微細化する作用を有する元素である。こうした効果を発揮させるためには、Cr含有量は0.05%以上とする必要がある。しかしながら、Cr含有量が過剰になると、粒界炭化物が粗大化して靱性を却って低下させるため、1.0%以下とする必要がある。尚、Cr含有量の好ましい下限は0.20%以上(より好ましくは0.30%以上)であり、好ましい上限は0.80%以下(より好ましくは0.70%以下)である。
Moは、粒界炭化物の粗大化と焼鈍軟化を抑制する上で重要な元素である。こうした効果を発揮させるためには、Mo含有量は0.10%以上とする必要がある。しかしながら、Mo含有量が過剰になると、SR焼鈍時に強度の過大な上昇により靱性を却って低下させるので、1.50%以下とする必要がある。尚、Mo含有量の好ましい下限は0.20%以上(より好ましくは0.30%以上)であり、好ましい上限は1.2%以下(より好ましくは1.0%以下)である。
Tiは、溶接時の微細組織生成の起点となる酸化物を形成し、溶接金属の靱性を向上させる上で有効な元素である。こうした効果を発揮させるためには、Ti含有量は0.040%以上とする必要がある。しかしながら、Ti含有量が過剰になると、SR焼鈍時に微細炭化物を形成して強度の過大な上昇により靱性を低下させるので、0.15%以下とする必要がある。尚、Ti含有量の好ましい下限は0.050%以上(より好ましくは0.055%以上)であり、好ましい上限は0.110%以下(より好ましくは0.090%以下)である。
Bは、溶接金属の強度、靱性に対して悪影響を及ぼす粒界フェライトの生成を抑制する上で有効な元素である。こうした効果を発揮させるためには、B含有量は0.0010%以上とする必要がある。しかしながら、B含有量が過剰になると、強度の過大な上昇をもたらし、靱性低下の原因となるので、0.0050%以下とする。尚、B含有量の好ましい下限は0.0012%以上(より好ましくは0.0015%以上)であり、好ましい上限は0.0045%以下(より好ましくは0.0040%以下)である。
Oは、溶接時の微細組織生成の起点となる酸化物を形成し、溶接金属の靱性を向上させるのに有用な元素である。こうした効果を発揮させるためには、O含有量は0.030%以上とする必要がある。しかしながら、O含有量が過剰になって0.100%を超えると、酸化物の粗大化を招き、靱性を却って低下させる。尚、O含有量の好ましい下限は0.035%以上(より好ましくは0.040%以上)であり、好ましい上限は0.080%以下(より好ましくは0.060%以下)である。
Nは、溶接金属中に不可避的に含まれる元素であり、その含有量を0%とすることは工業的に不可能である。しかしながら、N含有量が過剰になると、靱性に悪影響を及ぼすことになるので、0.015%以下とする必要がある。尚、N含有量の好ましい上限は0.010%以下(より好ましくは0.008%以下)である。
Cuは、溶接金属の強度を確保する上で有用な元素であるが、過剰に含有させるとSR焼鈍時に微細に析出することで強度を過大に上昇させ、靱性低下の原因となる。こうした観点から、Cuを含有させるときには、1.0%以下とすることが好ましい(より好ましくは0.80%以下)。尚、Cuを含有させることによる効果を有効に発揮させるためには、その含有量は0.05%以上(より好ましくは0.10%以上)とすることが好ましい。
Alは、溶接時の微細組織生成の起点となる酸化物を形成し、溶接金属の強度、靱性を向上させるのに有用な元素であるが、Al含有量が過剰になって0.030%を超えると、酸化物の粗大化を招き、靱性を却って低下させる。尚、Al含有量の好ましい下限は0.005%以上(より好ましくは0.010%以上)であり、好ましい上限は0.025%以下(より好ましくは0.020%以下)である。
母材板厚:20mm
開先角度:20°(V字型)
ルート間隔:16mm
溶接姿勢:下向き
シールドガス:20%CO2-80%Ar混合ガス(流量:25L/min)
入熱条件
ア)1.0kJ/mm(230A-25V,5.7mm/秒)
イ)1.6kJ/mm(280A-29V,5.1mm/秒)
ウ)2.0kJ/mm(280A-29V,4.1mm/秒)
エ)2.6kJ/mm(300A-31V,3.6mm/秒)
予熱-パス間温度:100~190℃
積層方法:6層12パス
SR焼鈍温度:600~680℃
SR焼鈍時間:2~10時間
SR焼鈍後の溶接金属の最終パス中央部よりレプリカTEM観察用試験片を採取し、7500倍にて13.3×15.7μmの視野を有する画像を4枚撮影した。画像解析ソフト(「Image-Pro Plus」 Media Cybernetics社製)により、円相当直径:0.40μm以上の炭化物を選択したうえで、粒界炭化物の平均円相当直径を算出した。この際、下記の方法で炭化物形態の解析を行った。
(2)上記直線Aiと交わる円相当直径が0.40μm以上の炭化物を選定し(図2C)、画像解析により平均円相当直径を算出する。図2Cには、選定された炭化物を符号1~11で示している。前記図2Bに示した直線A1は炭化物1、2、3と交わる直線である。同様に、直線A2は炭化物2、3、4と交わる直線、直線A3は炭化物3、4、5と交わる直線、直線A4は炭化物4、5、6と交わる直線、直線A5は炭化物5、8、9と交わる直線、直線A6は炭化物8、9、10と交わる直線、直線A7は、炭化物9、10、11と交わる直線、直線A8は炭化物8、6、7と交わる直線を夫々示している。
SR焼鈍処理を施した溶接金属の板厚中央部から、溶接方向に平行に引張試験片(JIS Z 2242:2005)に準拠した試験片を採取し(図3)、室温(25℃)において、JISZ 2241:1998の要領で、引張強度(TS)を測定した。引張強度(TS)>620MPaを強度に優れると評価した。
SR焼鈍処理を施した溶接金属の板厚中央部より、図4に基づき溶接線方向に垂直にシャルピー衝撃試験片(JIS Z3111 4号Vノッチ試験片)を採取し、JIS Z2242:2005の要領で、-40℃での吸収エネルギー(vE-40)を測定し、3回での平均値が60Jを超えるものを低温靱性に優れると評価した。
Claims (5)
- C :0.02~0.10%(「質量%」の意味。以下同じ)、
Si:0.10~0.60%、
Mn:0.90~2.5%、
Ni:0.20~2.00%、
Cr:0.05~1.0%、
Mo:0.10~1.50%、
Ti:0.040~0.15%、
B :0.0010~0.0050%、
O :0.030~0.100%、
N :0.015%以下(0%を含まない)を夫々含有し、
残部が鉄および不可避的不純物からなり、
溶接金属の粒界に存在する炭化物のうち、円相当直径で0.40μm以上の炭化物の平均円相当直径が0.75μm以下であることを特徴とする溶接金属。 - 更に他の元素として、Cu:1.0%以下(0%を含まない)およびV:0.40%以下(0%を含まない)の少なくとも1種を含有するものである請求項1に記載の溶接金属。
- 更に他の元素として、Al:0.030%以下(0%を含まない)を含有するものである請求項1に記載の溶接金属。
- 更に他の元素として、Al:0.030%以下(0%を含まない)を含有するものである請求項2に記載の溶接金属。
- 請求項1~4のいずれかに記載の溶接金属を備えた溶接構造体。
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US14/769,611 US20160008931A1 (en) | 2013-03-08 | 2014-02-24 | Weld metal and welded structure provided with same |
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CA2900744A CA2900744C (en) | 2013-03-08 | 2014-02-24 | Weld metal and welded structure provided with same |
EP14760921.8A EP2965857A4 (en) | 2013-03-08 | 2014-02-24 | WELDED METAL AND WELDED STRUCTURE THEREOF |
KR1020157023990A KR101778422B1 (ko) | 2013-03-08 | 2014-02-24 | 용접 금속 및 이것을 구비한 용접 구조체 |
CN201480011931.XA CN105026100B (zh) | 2013-03-08 | 2014-02-24 | 焊接金属及具备它的焊接结构体 |
RU2015142675A RU2623527C2 (ru) | 2013-03-08 | 2014-02-24 | Металл сварного шва и сварная конструкция с его использованием |
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WO2012137957A1 (ja) * | 2011-04-08 | 2012-10-11 | 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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RU2623527C2 (ru) | 2017-06-27 |
KR20150114561A (ko) | 2015-10-12 |
US20160008931A1 (en) | 2016-01-14 |
EP2965857A4 (en) | 2016-09-28 |
EP2965857A1 (en) | 2016-01-13 |
KR101778422B1 (ko) | 2017-09-13 |
EP3424637A1 (en) | 2019-01-09 |
CA2900744C (en) | 2017-01-03 |
CN105026100A (zh) | 2015-11-04 |
RU2015142675A (ru) | 2017-04-13 |
JP6211950B2 (ja) | 2017-10-11 |
CN105026100B (zh) | 2018-01-23 |
CA2900744A1 (en) | 2014-09-12 |
JP2014195832A (ja) | 2014-10-16 |
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