WO2016195028A1 - 溶接金属及び溶接構造体 - Google Patents
溶接金属及び溶接構造体 Download PDFInfo
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- WO2016195028A1 WO2016195028A1 PCT/JP2016/066442 JP2016066442W WO2016195028A1 WO 2016195028 A1 WO2016195028 A1 WO 2016195028A1 JP 2016066442 W JP2016066442 W JP 2016066442W WO 2016195028 A1 WO2016195028 A1 WO 2016195028A1
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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
- B23K35/36—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 relates to a weld metal and a welded structure.
- the equivalent circle diameter By defining the equivalent circle diameter, a weld metal that exhibits high strength and excellent low-temperature toughness after SR annealing can be realized.
- the toughness evaluation temperature of this weld metal is ⁇ 40 ° C., and it cannot be said that the toughness at ⁇ 60 ° C., which is a lower temperature, is guaranteed.
- Japanese Unexamined Patent Publication No. 2006-239733 Japanese Unexamined Patent Publication No. 9-253886 Japanese Unexamined Patent Publication No. 2014-195832
- the present invention has been made based on the above situation, and in a gas shielded arc welding using a flux cored wire, a weld metal capable of obtaining high strength and high toughness at ⁇ 60 ° C. or less after SR annealing, and The purpose is to provide a welded structure.
- the present inventors have found that the toughness at low temperatures becomes unstable when fine carbides produced during welding are present in the grains of the weld metal. From this, the present inventors controlled the chemical composition of the weld metal and controlled the size of the carbide generated in the weld metal during welding, thereby providing high strength and excellent low temperature toughness after SR annealing. It was found that a weld metal exhibiting Specifically, it has been found that Mo having an action of suppressing coarsening and annealing softening of grain boundary carbides may be added to the weld metal to control the chemical component composition.
- the weld metal has a structure in which many regions called “crystal grains” having different orientations are gathered.
- “Grain boundary” means the boundary between these crystal grains, and the ferrite grain boundary is Of course, it means a large-angle grain boundary including a prior austenite grain boundary, a block boundary, a packet boundary, and the like. Further, “inside the grain” means the entire region including the grain boundary of the crystal grain.
- C carbon: 0.02 mass% to 0.08 mass%
- Si silicon: 0.10 mass% to 0.30 mass%
- Mn manganese
- Ni nickel
- Cr chromium
- Mo mobdenum
- Ti titanium
- Ti titanium
- B boron
- O oxygen
- nitrogen 0.030% by mass or more and 0.100% by mass or less
- N nitrogen: more than 0% by mass and 0.015% by mass or less
- Nb (niobium) + V vanadium: 0 .008 mass% or more and 0.05 mass% or less
- the remaining Fe (iron)
- the weld metal can obtain high strength and toughness by setting the content of each composition within the above range. That is, high intensity
- the weld metal has an average equivalent circle diameter of 0.10 ⁇ m or more for carbides having an equivalent circle diameter of less than 0.40 ⁇ m in the grains, the toughness at low temperature is stable and high toughness at ⁇ 60 ° C. or less is obtained.
- the “circle equivalent diameter” means a diameter of a perfect circle having the same area as the area of carbide particles observed on an observation surface such as a transmission electron microscope (TEM: Transmission Electron Microscope).
- composition may further comprise at least one composition.
- strength and low-temperature toughness can be accelerated
- a welded structure having the above-mentioned weld metal.
- the welded structure has the weld metal, high strength and high toughness at ⁇ 60 ° C. or lower can be obtained.
- the weld metal and welded structure of the present invention can provide high strength and high toughness at ⁇ 60 ° C. or less after SR annealing in gas shielded arc welding using a flux cored wire.
- the weld metal has an average equivalent circle diameter of a carbide having an equivalent circle diameter of less than 0.40 ⁇ m of 0.10 ⁇ m or more.
- the lower limit of the average equivalent circle diameter of the carbide having an equivalent circle diameter of less than 0.40 ⁇ m is 0.10 ⁇ m as described above, preferably 0.15 ⁇ m, 20 ⁇ m is more preferable.
- the carbide size is remarkably refined, and the average equivalent circle diameter of the carbide may not be evaluated even by the measurement method of the average equivalent circle diameter of the carbide, which will be described later.
- the average equivalent circle diameter is less than 0.10 ⁇ m ”.
- the weld metal is present at the grain boundary, and the average equivalent circle diameter of carbide having an equivalent circle diameter of 0.40 ⁇ m or more is 0.75 ⁇ m or less.
- the grain boundary carbide produced at the grain boundary tends to be coarser than the carbide in the grain.
- the prior austenite grain boundaries become brittle by annealing, cracks tend to preferentially propagate from the prior austenite grain boundaries. Therefore, if coarse carbides are present in the prior austenite grain boundaries, cracks are likely to occur starting from them, and the toughness is significantly reduced during SR annealing in combination with the embrittlement phenomenon due to annealing.
- the grain boundary carbide is kept fine as described above, the weld metal has excellent low temperature toughness after SR annealing.
- the upper limit of the average equivalent circle diameter of carbides having an equivalent circle diameter of 0.40 ⁇ m or more is 0.75 ⁇ m as described above, preferably 0.70 ⁇ m, .65 ⁇ m is more preferable.
- the grain boundary carbide size is remarkably refined, and the average equivalent circle diameter of the grain boundary carbide may not be evaluated even by the measurement method of the average equivalent circle diameter of the grain boundary carbide described later.
- the average equivalent circle diameter of the grain boundary carbides of 0.40 ⁇ m or more is 0.75 ⁇ m or less ”.
- the weld metal is C (carbon): 0.02 mass% or more and 0.08 mass% or less, Si (silicon): 0.10 mass% or more and 0.30 mass% or less, Mn (manganese): 1.20 mass % To 2.0% by mass, Ni (nickel): 0.50% to 3.00% by mass, Cr (chromium): 0% to 0.70% by mass, Mo (molybdenum): 0.
- [C (carbon)] C is an element that ensures the strength of the weld metal after SR annealing.
- the lower limit of the C content of the weld metal is 0.02% by mass, preferably 0.03% by mass, and more preferably 0.04% by mass.
- the upper limit of the C content of the weld metal is 0.08% by mass, and preferably 0.07% by mass. If the C content of the weld metal is smaller than the lower limit, a predetermined strength may not be obtained after SR annealing. Conversely, if the C content of the weld metal exceeds the above upper limit, the grain boundary carbides become coarse during SR annealing, and the toughness of the weld metal may be reduced.
- Si (silicon)] Si is an element that ensures the strength of the weld metal after SR annealing.
- the lower limit of the Si content of the weld metal is 0.10% by mass, preferably 0.12% by mass, and more preferably 0.15% by mass.
- the upper limit of the Si content of the weld metal is 0.30 mass%, preferably 0.25 mass%, and more preferably 0.20 mass%. If the Si content of the weld metal is smaller than the lower limit, a predetermined strength may not be obtained after SR annealing.
- the Si content of the weld metal exceeds the above upper limit, it promotes temper embrittlement during SR annealing and promotes the formation of a hard second phase that adversely affects low-temperature toughness. There is a risk of lowering.
- Mn is an element that forms an oxide serving as a starting point for generating a microstructure during welding and improves the strength and low-temperature toughness of the weld metal.
- the lower limit of the Mn content of the weld metal is 1.20% by mass, preferably 1.30% by mass, and more preferably 1.40% by mass.
- the upper limit of the Mn content of the weld metal is 2.0 mass%, preferably 1.8 mass%, and more preferably 1.7 mass%. If the Mn content of the weld metal is smaller than the lower limit, oxides are hardly formed, and the strength and low temperature toughness of the weld metal may not be sufficiently improved. Conversely, if the Mn content of the weld metal exceeds the above upper limit, temper embrittlement during SR annealing is promoted, and the toughness of the weld metal may be reduced.
- Ni is an element effective for improving the low temperature toughness of the weld metal.
- the lower limit of the Ni content of the weld metal is 0.50 mass%, preferably 0.60 mass%, and more preferably 0.70 mass%.
- the upper limit of the Ni content of the weld metal is 3.00% by mass, preferably 2.80% by mass, and more preferably 2.60% by mass. If the Ni content of the weld metal is smaller than the lower limit, the low temperature toughness of the weld metal may not be sufficiently improved. Conversely, if the Ni content of the weld metal exceeds the upper limit, it is considered that the weld metal may not obtain a predetermined toughness after SR annealing, such as lowering the upper shelf energy in the Charpy test.
- [Cr (chrome)] Cr is an element having an effect of refining grain boundary carbides during SR annealing.
- the Cr content may be 0% by mass. Therefore, the lower limit of the Cr content of the weld metal is 0% by mass, preferably 0.20% by mass, and more preferably 0.30% by mass.
- the upper limit of the Cr content of the weld metal is 0.70 mass%, preferably 0.65 mass%, and more preferably 0.60 mass%.
- the grain boundary carbides are not refined during SR annealing, and the toughness of the weld metal may not be sufficiently improved. Conversely, if the Cr content of the weld metal exceeds the upper limit, the grain boundary carbides are coarsened and the toughness of the weld metal may be lowered.
- Mo molecular (molybdenum)
- Mo is an element that suppresses coarsening and annealing softening of grain boundary carbides by fine precipitation in the weld metal grains.
- the lower limit of the Mo content of the weld metal is 0.10% by mass, preferably 0.20% by mass, and more preferably 0.30% by mass.
- the upper limit of the Mo content of the weld metal is 0.70 mass%, preferably 0.65 mass%, and more preferably 0.60 mass%. If the Mo content of the weld metal is smaller than the lower limit, coarsening of grain boundary carbides and annealing softening may not be sufficiently suppressed. Conversely, if the Mo content of the weld metal exceeds the upper limit, the strength of the weld metal is excessively increased by precipitating fine carbides during SR annealing, which may reduce the toughness at low temperatures. is there.
- Ti is an element that forms an oxide serving as a starting point for generating a microstructure during welding and improves the toughness of the weld metal.
- the lower limit of the Ti content of the weld metal is 0.04% by mass, preferably 0.05% by mass, and more preferably 0.055% by mass.
- the upper limit of the Ti content of the weld metal is 0.08 mass%, preferably 0.075 mass%, and more preferably 0.07 mass%. If the Ti content of the weld metal is smaller than the lower limit, an oxide is hardly formed, and the toughness of the weld metal may not be sufficiently improved. On the other hand, if the Ti content of the weld metal exceeds the upper limit, the strength of the weld metal is excessively increased by precipitating fine carbides during SR annealing, thereby reducing the toughness at low temperatures. is there.
- [B (boron)] B is an element that suppresses the formation of grain boundary ferrite that adversely affects the strength and toughness of the weld metal.
- the lower limit of the B content of the weld metal is 0.0010% by mass, preferably 0.0012% by mass, and more preferably 0.0015% by mass.
- the upper limit of the B content of the weld metal is 0.0050 mass%, preferably 0.0045 mass%, and more preferably 0.0040 mass%. If the B content of the weld metal is smaller than the above lower limit, the formation of grain boundary ferrite cannot be sufficiently suppressed, and the predetermined strength and toughness of the weld metal may not be ensured. Conversely, if the B content of the weld metal exceeds the upper limit, the strength of the weld metal may increase excessively and the toughness may decrease.
- [O (oxygen)] O is an element that forms an oxide serving as a starting point for generating a microstructure during welding and improves the toughness of the weld metal.
- the lower limit of the O content of the weld metal is 0.030% by mass, preferably 0.035% by mass, and more preferably 0.040% by mass.
- the upper limit of the O content of the weld metal is 0.100% by mass, preferably 0.080% by mass, and more preferably 0.060% by mass. If the O content of the weld metal is smaller than the lower limit, oxides are not sufficiently formed, and the predetermined toughness of the weld metal may not be ensured. On the other hand, when the O content of the weld metal exceeds the upper limit, the oxide is coarsened, and the toughness of the weld metal may be reduced.
- N (nitrogen) N is an element inevitably contained in the weld metal, and it is industrially impossible to make its content 0 mass%. Therefore, the N content of the weld metal is more than 0% by mass.
- the upper limit of the N content of the weld metal is 0.015% by mass, preferably 0.010% by mass, and more preferably 0.008% by mass. When the N content of the weld metal exceeds the upper limit, the toughness of the weld metal may be reduced.
- Nb and V are elements that suppress coarsening of grain boundary carbides.
- the lower limit of the total content of Nb and V in the weld metal is 0.008% by mass, preferably 0.010% by mass, and more preferably 0.012% by mass.
- the upper limit of the total content of Nb and V in the weld metal is 0.05% by mass, preferably 0.045% by mass, and more preferably 0.040% by mass. If the total content of Nb and V is smaller than the above lower limit, coarsening of grain boundary carbides may not be sufficiently suppressed. On the other hand, if the total content of Nb and V exceeds the upper limit, the strength of the weld metal is excessively increased by precipitation of fine carbides during SR annealing, which may reduce toughness at low temperatures. is there.
- the weld metal has C, Si, Mn, Ni, Cr, Mo, Ti, B, O, N, Nb, and V as basic components. Moreover, the said weld metal contains Fe and an unavoidable impurity in the remainder other than the said basic component.
- the inevitable impurities for example, inclusion of elements such as P (phosphorus), S (sulfur), and Sn (tin) brought in depending on the status of raw materials, materials, manufacturing facilities, and the like is allowed.
- P is an element that remarkably promotes temper embrittlement during SR annealing, so it is preferably suppressed to at least 0.010% by mass or less.
- the weld metal may contain, for example, Cu as another element other than the basic component.
- Cu is an element useful for ensuring the strength of the weld metal.
- As Cu content of the said weld metal more than 0 mass% is preferable, and 0.05 mass% is preferable as a minimum of Cu content, and 0.10 mass% is more preferable.
- the upper limit of the Cu content of the weld metal is preferably 1.0% by mass, and more preferably 0.8% by mass. If the Cu content of the weld metal is smaller than the above lower limit, the effect of improving the strength of the weld metal may be insufficient. Conversely, if the Cu content of the weld metal exceeds the upper limit, the strength of the weld metal may be excessively increased, leading to a decrease in toughness.
- the weld metal may contain Co as an element other than the basic component.
- Co is an element useful for ensuring the strength of the weld metal.
- the Co content of the weld metal is preferably more than 0% by mass, and the lower limit of the Co content is preferably 0.05% by mass, more preferably 0.10% by mass.
- the upper limit of the Co content of the weld metal is preferably 1.0% by mass, and more preferably 0.8% by mass. If the Co content of the weld metal is less than the lower limit, the effect of improving the strength of the weld metal may be insufficient. On the contrary, if the Co content of the weld metal exceeds the upper limit, the strength of the weld metal may be excessively increased and the toughness may be reduced.
- the weld metal may contain Al as an element other than the basic component.
- Al is an element that forms an oxide serving as a starting point for generating a microstructure during welding and improves the strength and toughness of the weld metal.
- the Al content of the weld metal is preferably more than 0% by mass, and the lower limit of the Al content is preferably 0.005% by mass and more preferably 0.010% by mass.
- the upper limit of the Al content of the weld metal is preferably 0.030% by mass, more preferably 0.025% by mass, and still more preferably 0.020% by mass.
- the Al content of the weld metal is smaller than the lower limit, oxides are not sufficiently formed, and the effect of improving the strength and toughness of the weld metal may be insufficient. On the contrary, when the Al content of the weld metal exceeds the upper limit, the oxide is coarsened and the toughness of the weld metal may be lowered.
- the Cu, Co, and Al may be contained singly or in combination.
- X value ([Mo] + [Ti] + [Nb] + 2 ⁇ [V]) / [C] (1)
- FCW flux cored wire
- the welding material component is naturally limited 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 contents [mass%] of C, Mo, Ti, Nb, and V are set to [C], [Mo], [Ti], [Nb], and [V], respectively.
- the degree of influence of toughness reduction at low temperatures can be defined by the Y value of the following formula (2).
- the lower limit of the Y value is preferably 12, and more preferably 12.5.
- the upper limit of the Y value is preferably 20, and more preferably 19.5. If the Y value is smaller than the above lower limit, the growth of carbides in the grains tends to be inhibited, and the carbides in the grains may be refined.
- Y value ⁇ [Mo] + ([Ti] -4) + [Nb] + 2 ⁇ [V] ⁇ / [C] (2)
- the lower limit of the ratio of metal Si content [% by mass] to SiO 2 content [% by mass] of the flux cored wire is preferably 0.90, more preferably 0.93, and 1.00. Is more preferable.
- the upper limit of the ratio is preferably 3.0 and more preferably 2.5. If the ratio is less than the lower limit, the solute Si is insufficient, leading to instability of the carbide, and the grain equivalent carbide size is increased to increase the mean equivalent circle diameter of the grain boundary carbide having a circle equivalent diameter of 0.40 ⁇ m or more. May not be kept below the above upper limit. Conversely, if the ratio exceeds the upper limit, workability during welding may be reduced.
- the lower limit of the heat input is preferably 0.7 kJ / mm, more preferably 1.0 kJ / mm.
- the upper limit of the heat input is preferably 2.5 kJ / mm, more preferably 2.0 kJ / mm, and still more preferably 1.6 kJ / mm. If the heat input is less than the lower limit, the construction efficiency during welding may be reduced. Conversely, if the heat input exceeds the above upper limit, the cooling rate during welding decreases and the strength of the predetermined weld metal cannot be obtained, and carbide is generated during cooling, and this carbide grows during SR annealing. Therefore, the desired grain boundary carbide form may not be obtained. As a result, the toughness of the weld metal after SR annealing may be reduced.
- the lower limit of the preheating temperature and the interpass temperature is preferably 100 ° C., more preferably 120 ° C.
- an upper limit of preheating temperature and interpass temperature 180 degreeC is preferable and 160 degreeC is more preferable. If the preheating temperature and the interpass temperature are smaller than the lower limits, there is a risk that low temperature cracking is likely to occur. Conversely, if the preheating temperature and the interpass temperature exceed the above upper limits, the cooling rate at the time of welding decreases, and the strength of the predetermined weld metal cannot be obtained, and carbide is generated during cooling, and this carbide is subjected to SR annealing. Occasionally, the desired grain boundary carbide form may not be obtained by growing. As a result, the toughness of the weld metal after SR annealing may be reduced.
- annealing conditions such as SR annealing temperature and SR annealing time, what is necessary is just to follow according to the conditions currently performed conventionally, but from a viewpoint of control of a grain boundary carbide, these conditions can be set as follows. preferable.
- the lower limit of the SR annealing temperature is preferably 580 ° C., more preferably 600 ° C.
- an upper limit of SR annealing temperature 680 degreeC is preferable and 650 degreeC is more preferable. If the SR annealing temperature is lower than the lower limit, the stress generated during welding may not be sufficiently removed. Conversely, if the SR annealing temperature exceeds the above upper limit, coarsening of the grain boundary carbide during SR annealing is promoted and a desired grain boundary carbide form cannot be obtained, and as a result, the toughness of the weld metal after SR annealing is increased. May decrease.
- the lower limit of the SR annealing time is preferably 2 hours, and more preferably 3 hours.
- the upper limit of the SR annealing time is preferably 12 hours, and more preferably 10 hours. If the SR annealing time is smaller than the lower limit, the stress generated during welding may not be sufficiently removed. Conversely, if the SR annealing time exceeds the above upper limit, coarsening of the grain boundary carbide during SR annealing is promoted and the desired grain boundary carbide form cannot be obtained, and as a result, the toughness of the weld metal after SR annealing is increased. May decrease.
- the weld structure has the weld metal.
- the welded structure having the weld metal is obtained by welding a predetermined member under the welding conditions. Since the weld structure includes the weld metal, high strength and high toughness at ⁇ 60 ° C. or less can be ensured. As a result, the reliability and durability of the welded structure used during the drilling and production of the subsea oil field are improved.
- the weld metal has an average equivalent circle diameter of 0.10 ⁇ m or more for carbides having an equivalent circle diameter of less than 0.40 ⁇ m in the grains, the toughness at low temperature is stable and high toughness at ⁇ 60 ° C. or less is obtained. .
- a plurality of flux cored wires having a wire diameter of ⁇ 1.2 mm and a flux filling rate of 15.5% by mass were produced.
- 31 types of flux cored wires of welding materials 3F1 to 3F31 having different composition components were produced.
- “Others” is the balance and is the content of Fe and inevitable impurities.
- “-” indicates that the component is not contained.
- an SM490A steel plate having an average plate thickness of 20 mm processed into a groove shape shown in FIG. 1-No. 32 weld metals were obtained.
- the groove angle is 20 ° in a V shape
- the root interval is 16 mm
- the welding posture is downward
- the heat input condition is one of the following
- the preheating temperature and the interpass temperature are 140 ° C. or higher and 190 ° C. or lower.
- each of the produced weld metals was subjected to a heat treatment with an SR annealing temperature of 620 ° C. or more and 680 ° C. or less and an SR annealing time of 2 hours or more and 8 hours or less.
- Table 2 shows the welding conditions of each of the produced weld metals. A) 1.0kJ / mm, 230A-25V, 5.7mm / sec B) 1.6kJ / mm, 280A-29V, 5.1mm / sec C) 2.0 kJ / mm, 280A-29V, 4.1 mm / sec
- a straight line Ai 1, 2, 3,... N, n: total number of straight lines intersecting with at least three carbides having a circle equivalent diameter of 0.40 ⁇ m or more and having a length of 6 ⁇ m.
- a region B indicated by a broken-line circle indicates a standard of the size of the target carbide, and is an imaginary size of a perfect circle having a diameter of 0.40 ⁇ m. is there.
- the filled area C indicates carbide with an equivalent circle diameter of 0.40 ⁇ m or more
- the shaded area D indicates carbide with an equivalent circle diameter of less than 0.40 ⁇ m. Yes.
- the straight line shown with the broken line of FIG. 2B is a straight line exceeding 6 micrometers in length.
- a straight line that intersects only two or less carbides having a circle equivalent diameter of 0.40 ⁇ m or more among straight lines having a length of 6 ⁇ m is not included in the straight line Ai.
- a straight line A1 shown in FIG. 2B is a straight line intersecting with 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 A straight line that intersects with carbides 8, 9, and 10, a straight line A7 that intersects with carbides 8, 9, 10, and 11, and a straight line A8 that intersects with carbides 8, 6, and 7, respectively.
- Table 2 shows the results of the average equivalent circle diameter of the grain boundary carbides calculated by this method.
- the average equivalent circle diameter is It is evaluated as satisfying “0.75 ⁇ m or less”.
- the absorbed energy vE ⁇ 40 and vE ⁇ 60 at ⁇ 40 ° C. and ⁇ 60 ° C. shown in Table 2 are both average values of three measurements. Further, the absorbed energy vE ⁇ 40 at ⁇ 40 ° C. is shown as a reference, and it can be judged that those exceeding 60 J are excellent in toughness at a relatively low temperature.
- No. 1 satisfies the range of the composition component of the present invention, and the form of carbide in the grains and at the grain boundaries satisfies the definition of the present invention.
- the weld metal of No. 20 has a tensile strength TS exceeding 620 MPa and an absorption energy vE ⁇ 60 at ⁇ 60 ° C. exceeding 40 J, and it can be said that both strength and low temperature toughness can be achieved at a high level after SR annealing. Further, these weld metals have an absorption energy vE ⁇ 40 at ⁇ 40 ° C. exceeding 60 J, and it can be seen that sufficient toughness can be obtained even in a temperature range of ⁇ 40 ° C.
- 21-No. No. 30 has an absorption energy vE ⁇ 60 at ⁇ 60 ° C. of 40 J or less, and it can be seen that sufficient toughness cannot be obtained at low temperatures.
- the average equivalent circle diameter of carbide with an equivalent circle diameter of less than 0.40 ⁇ m is as small as 0.05 ⁇ m, so the absorbed energy vE ⁇ 60 at ⁇ 60 ° C. is 40 J or less, and sufficient toughness at low temperature is obtained. It is thought that it was not obtained.
- the weld metal and welded structure have high strength after SR annealing and high toughness at ⁇ 60 ° C. or less in gas shielded arc welding using a flux cored wire. It can be suitably used as an offshore structure or the like that is constructed during the drilling and production of a subsea oil field.
- Carbide A1 to A8 Straight line B True circle C having a diameter of 0.40 ⁇ m Carbide having an equivalent circle diameter of 0.40 ⁇ m or more D Carbide having an equivalent circle diameter of less than 0.40 ⁇ m
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Abstract
Description
当該溶接金属は、円相当直径が0.40μm未満の炭化物の平均円相当直径が0.10μm以上である。
当該溶接金属は、C(炭素):0.02質量%以上0.08質量%以下、Si(ケイ素):0.10質量%以上0.30質量%以下、Mn(マンガン):1.20質量%以上2.0質量%以下、Ni(ニッケル):0.50質量%以上3.00質量%以下、Cr(クロム):0質量%以上0.70質量%以下、Mo(モリブデン):0.10質量%以上0.70質量%以下、Ti(チタン):0.04質量%以上0.08質量%以下、B(ホウ素):0.0010質量%以上0.0050質量%以下、O(酸素):0.030質量%以上0.100質量%以下、N(窒素):0質量%超0.015質量%以下、Nb(ニオブ)+V(バナジウム):0.008質量%以上0.05質量%以下、並びに残部:Fe(鉄)及び不可避的不純物である組成を有する。
Cは、SR焼鈍後における当該溶接金属の強度を確保する元素である。当該溶接金属のC含有量の下限としては、0.02質量%であり、0.03質量%が好ましく、0.04質量%がより好ましい。一方、当該溶接金属のC含有量の上限としては、0.08質量%であり、0.07質量%が好ましい。当該溶接金属のC含有量が上記下限より小さいと、SR焼鈍後に所定の強度が得られないおそれがある。逆に、当該溶接金属のC含有量が上記上限を超えると、SR焼鈍時に粒界炭化物の粗大化を招き、当該溶接金属の靱性が低下するおそれがある。
Siは、SR焼鈍後における当該溶接金属の強度を確保する元素である。当該溶接金属のSi含有量の下限としては、0.10質量%であり、0.12質量%が好ましく、0.15質量%がより好ましい。一方、当該溶接金属のSi含有量の上限としては、0.30質量%であり、0.25質量%が好ましく、0.20質量%がより好ましい。当該溶接金属のSi含有量が上記下限より小さいと、SR焼鈍後に所定の強度が得られないおそれがある。逆に、当該溶接金属のSi含有量が上記上限を超えると、SR焼鈍時の焼戻し脆化を助長すると共に低温靭性に悪影響を及ぼす硬質第二相の生成を助長し、当該溶接金属の靭性の低下を招くおそれがある。
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、当該溶接金属の強度及び低温靱性を向上させる元素である。当該溶接金属のMn含有量の下限としては、1.20質量%であり、1.30質量%が好ましく、1.40質量%がより好ましい。一方、当該溶接金属のMn含有量の上限としては、2.0質量%であり、1.8質量%が好ましく、1.7質量%がより好ましい。当該溶接金属のMn含有量が上記下限より小さいと、酸化物が形成され難くなり、当該溶接金属の強度及び低温靱性を十分に向上できないおそれがある。逆に、当該溶接金属のMn含有量が上記上限を超えると、SR焼鈍時の焼戻し脆化を助長し、当該溶接金属の靭性の低下を招くおそれがある。
Niは、当該溶接金属の低温靱性向上に有効な元素である。当該溶接金属のNi含有量の下限としては、0.50質量%であり、0.60質量%が好ましく、0.70質量%がより好ましい。一方、当該溶接金属のNi含有量の上限としては、3.00質量%であり、2.80質量%が好ましく、2.60質量%がより好ましい。当該溶接金属のNi含有量が上記下限より小さいと、当該溶接金属の低温靱性を十分に向上できないおそれがある。逆に、当該溶接金属のNi含有量が上記上限を超えると、シャルピー試験における上部棚エネルギーが低下する等、SR焼鈍後において当該溶接金属が所定の靱性を得られなくなるおそれがあると考えられる。
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。但し、当該溶接金属は、粒界炭化物の微細化作用を有する他元素が十分に添加されているため、Cr含有量が0質量%であってもよい。そのため、当該溶接金属のCr含有量の下限としては、0質量%であり、0.20質量%が好ましく、0.30質量%がより好ましい。一方、当該溶接金属のCr含有量の上限としては、0.70質量%であり、0.65質量%が好ましく、0.60質量%がより好ましい。当該溶接金属のCr含有量が上記下限より小さいと、SR焼鈍時に粒界炭化物が微細化せず、当該溶接金属の靱性を十分に向上できないおそれがある。逆に、当該溶接金属のCr含有量が上記上限を超えると、粒界炭化物が粗大化して当該溶接金属の靱性が却って低下するおそれがある。
Moは、溶接金属の粒内への微細析出により粒界炭化物の粗大化と焼鈍軟化とを抑制する元素である。当該溶接金属のMo含有量の下限としては、0.10質量%であり、0.20質量%が好ましく、0.30質量%がより好ましい。一方、当該溶接金属のMo含有量の上限としては、0.70質量%であり、0.65質量%が好ましく、0.60質量%がより好ましい。当該溶接金属のMo含有量が上記下限より小さいと、粒界炭化物の粗大化と焼鈍軟化とを十分に抑制できないおそれがある。逆に、当該溶接金属のMo含有量が上記上限を超えると、SR焼鈍時に微細な炭化物を析出することにより当該溶接金属の強度が過大に上昇し、これにより低温での靭性を低下させるおそれがある。
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、当該溶接金属の靱性を向上させる元素である。当該溶接金属のTi含有量の下限としては、0.04質量%であり、0.05質量%が好ましく、0.055質量%がより好ましい。一方、当該溶接金属のTi含有量の上限としては、0.08質量%であり、0.075質量%が好ましく、0.07質量%がより好ましい。当該溶接金属のTi含有量が上記下限より小さいと、酸化物が形成され難くなり、当該溶接金属の靱性を十分に向上できないおそれがある。逆に、当該溶接金属のTi含有量が上記上限を超えると、SR焼鈍時に微細な炭化物を析出することにより当該溶接金属の強度が過大に上昇し、これにより低温での靭性を低下させるおそれがある。
Bは、当該溶接金属の強度及び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元素である。当該溶接金属のB含有量の下限としては、0.0010質量%であり、0.0012質量%が好ましく、0.0015質量%がより好ましい。一方、当該溶接金属のB含有量の上限としては、0.0050質量%であり、0.0045質量%が好ましく、0.0040質量%がより好ましい。当該溶接金属のB含有量が上記下限より小さいと、粒界フェライトの生成を十分に抑制できず、当該溶接金属の所定の強度及び靱性を整確保できないおそれがある。逆に、当該溶接金属のB含有量が上記上限を超えると、当該溶接金属の強度が過大に上昇し、靭性が低下するおそれがある。
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、当該溶接金属の靱性を向上させる元素である。当該溶接金属のO含有量の下限としては、0.030質量%であり、0.035質量%が好ましく、0.040質量%がより好ましい。一方、当該溶接金属のO含有量の上限としては、0.100質量%であり、0.080質量%が好ましく、0.060質量%がより好ましい。当該溶接金属のO含有量が上記下限より小さいと、酸化物が十分に形成されず、当該溶接金属の所定の靱性を確保できないおそれがある。逆に、当該溶接金属のO含有量が上記上限を超えると、酸化物の粗大化を招き、当該溶接金属の靱性を却って低下させるおそれがある。
Nは、当該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質量%とすることは工業的に不可能である。従って、当該溶接金属のN含有量は、0質量%超である。一方、当該溶接金属のN含有量の上限としては、0.015質量%であり、0.010質量%が好ましく、0.008質量%がより好ましい。当該溶接金属のN含有量が上記上限を超えると、当該溶接金属の靱性が低下するおそれがある。
Nb及びVは、粒界炭化物の粗大化を抑制する元素である。当該溶接金属におけるNb及びVの合計含有量の下限としては、0.008質量%であり、0.010質量%が好ましく、0.012質量%がより好ましい。一方、当該溶接金属におけるNb及びVの合計含有量の上限としては、0.05質量%であり、0.045質量%が好ましく、0.040質量%がより好ましい。Nb及びVの合計含有量が上記下限より小さいと、粒界炭化物の粗大化を十分に抑制できないおそれがある。逆に、Nb及びVの合計含有量が上記上限を超えると、SR焼鈍時に微細な炭化物を析出することにより当該溶接金属の強度が過大に上昇し、これにより低温での靭性を低下させるおそれがある。
当該溶接金属は、基本成分以外のその他の元素として例えばCuを含有してもよい。Cuは、当該溶接金属の強度を確保する上で有用な元素である。当該溶接金属のCu含有量としては、0質量%超が好ましく、Cu含有量の下限としては、0.05質量%が好ましく、0.10質量%がより好ましい。一方、当該溶接金属のCu含有量の上限としては、1.0質量%が好ましく、0.8質量%がより好ましい。当該溶接金属のCu含有量が上記下限より小さいと、当該溶接金属の強度の向上効果が不十分となるおそれがある。逆に、当該溶接金属のCu含有量が上記上限を超えると、当該溶接金属の強度を過大に上昇させ、靱性の低下を招くおそれがある。
また、当該溶接金属は、基本成分以外のその他の元素としてCoを含有してもよい。Coは、当該溶接金属の強度を確保する上で有用な元素である。当該溶接金属のCo含有量としては、0質量%超が好ましく、Co含有量の下限としては、0.05質量%が好ましく、0.10質量%がより好ましい。一方、当該溶接金属のCo含有量の上限としては、1.0質量%が好ましく、0.8質量%がより好ましい。当該溶接金属のCo含有量が上記下限より小さいと、当該溶接金属の強度の向上効果が不十分となるおそれがある。逆に、当該溶接金属のCo含有量が上記上限を超えると、当該溶接金属の強度を過大に上昇させ、靱性の低下を招くおそれがある。
さらに、当該溶接金属は、基本成分以外のその他の元素としてAlを含有してもよい。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、当該溶接金属の強度及び靱性を向上させる元素である。当該溶接金属のAl含有量としては、0質量%超が好ましく、Al含有量の下限としては、0.005質量%が好ましく、0.010質量%がより好ましい。一方、当該溶接金属のAl含有量の上限としては、0.030質量%が好ましく、0.025質量%がより好ましく、0.020質量%がさらに好ましい。当該溶接金属のAl含有量が上記下限より小さいと、酸化物が十分に形成されず、当該溶接金属の強度及び靱性の向上効果が不十分となるおそれがある。逆に、当該溶接金属のAl含有量が上記上限を超えると、酸化物の粗大化を招き、却って当該溶接金属の靭性が低下するおそれがある。
当該溶接金属において、粒内の炭化物を構成する主要元素であるC、Mo、Ti、Nb及びVのそれぞれの含有量[質量%]を[C]、[Mo]、[Ti]、[Nb]及び[V]とした場合、これらの各元素の低温靱性に及ぼす影響度合を加味して、低温時における靱性低下の影響度を下記式(1)のX値で規定できる。X値の下限としては、9が好ましく、10がより好ましい。一方、X値の上限としては、14が好ましく、13がより好ましい。X値が上記下限より小さいと、粒内の炭化物の成長が阻害される傾向にあり、粒内の炭化物が微細化するおそれがある。逆に、X値が上記上限を超えると、粒内の炭化物の核生成が促進される傾向にあり、粒内の炭化物が微細化するおそれがある。
X値=([Mo]+[Ti]+[Nb]+2×[V])/[C] ・・・(1)
当該溶接金属を得るための溶接方法としては、フラックスコアドワイヤ(FCW)を用いたガスシールドアーク溶接が好ましい。このようにアーク溶接法を適用することによって、溶接時の作業効率を向上できる。
Y値={[Mo]+([Ti]-4)+[Nb]+2×[V]}/[C] ・・・(2)
当該溶接構造体は、上記溶接金属を有する。例えば海底油田の掘削及び生産時に用いられる溶接構造物を製造する際、上記溶接条件で所定の部材を溶接することで上記溶接金属を有する当該溶接構造体が得られる。当該溶接構造体は、上記溶接金属を有するため、高い強度及び-60℃以下での高い靱性を確保することができる。その結果、海底油田の掘削及び生産時に用いられる溶接構造物などの信頼性、耐久性などが向上する。
当該溶接金属は、焼鈍軟化を抑制する作用を有するMoを含有することで、高い強度が得られる。また、当該溶接金属は、所定量のMoと所定合計量のNb及びVとを含有することにより粒界炭化物の粗大化を抑制できる。また、当該溶接金属は、上記粒界炭化物の粗大化の抑制効果等により、円相当直径が0.40μm以上の粒界炭化物の平均円相当直径が0.75μm以下なので、粗大な粒界炭化物を起点とする亀裂が発生し難く、SR焼鈍時における靱性の低下が抑制される。また、当該溶接金属は、粒内における円相当直径が0.40μm未満の炭化物の平均円相当直径が0.10μm以上なので、低温における靭性が安定し、-60℃以下での高い靱性が得られる。
ア)1.0kJ/mm、230A-25V、5.7mm/sec
イ)1.6kJ/mm、280A-29V、5.1mm/sec
ウ)2.0kJ/mm、280A-29V、4.1mm/sec
試験No.1~No.32について、熱処理後の開先部に形成された各溶接金属の中央部を切り出し、化学成分分析を行った。この化学分析により各溶接金属において得られた各元素の組成含有量を表2に示す。なお、表2中「-」は、その成分を含有しないことを示す。
熱処理後の溶接金属の最終パス中央部より粒界が露出するレプリカTEM観察用試験片を採取し、7,500倍にて13.3×15.7μmの視野を有する画像を4枚撮影した。これらの画像について、画像解析ソフト(Media Cybernetics社の「Image-Pro Plus」)により円相当直径0.40μm以上の炭化物を選択した上で、粒界炭化物の平均円相当直径を算出した。具体的には、以下の方法で円相当直径が0.40μm以上の粒界炭化物の平均円相当直径を求めた。
熱処理後の溶接金属の粒内よりレプリカTEM観察用試験片を採取し、上記円相当直径が0.40μm以上の粒界炭化物の平均円相当直径の測定と同様の方法により、円相当直径が0.40μm未満の炭化物の平均円相当直径を算出した。すなわち、粒内において上記方法で円相当直径0.40μm以上の炭化物と選択されなかった炭化物について、画像解析により平均円相当直径を算出した。この方法により算出した炭化物の平均円相当直径の結果を表2に示す。
強度評価として、各溶接金属について引張試験を実施した。この引張試験では、図3に示すように熱処理後の各溶接金属の板厚中央部より溶接線方向に平行にJIS-Z2202(1988)に準拠した試験片を採取した。この試験片について、JIS-Z2241(2011)に準拠して室温25℃で引張強さ(TS:Tensile Strength)を測定した。この試験では、引張強さTSが620MPaを超えるものを強度に優れると評価した。これらの引張強さの測定結果を表2に示す。なお、図3中で長さを表す数値の単位はmmである。
低温靭性の評価では、熱処理後の各溶接金属の板厚中央部より図4に基づき溶接線方向と垂直方向に、JIS-Z3111(2005)の4号Vノッチ試験片をシャルピー衝撃試験片として採取した。この試験片について、JIS-Z2242(2005)に準拠して-40℃及び-60℃でシャルピー衝撃試験を実施した。この試験では、3回の測定の平均値で、-60℃における吸収エネルギーvE-60が40Jを超えるものを低温での靭性に優れると評価した。これらの低温靭性の測定結果を表2に示す。なお、表2に示す-40℃及び-60℃での吸収エネルギーvE-40、vE-60 は、いずれも3回の測定の平均値である。また、-40℃における吸収エネルギーvE-40 は、参考として示すもので、60Jを超えるものを比較的低温での靭性に優れると判断できる。
表2より、本発明の組成成分の範囲を満たし、かつ粒内及び粒界における炭化物の形態が本発明の規定を満たすNo.1~No.20の溶接金属は、引張強さTSが620MPaを超え、-60℃での吸収エネルギーvE-60 が40Jを超えており、SR焼鈍後に高レベルで強度及び低温での靱性を両立できるといえる。また、これらの溶接金属は、-40℃での吸収エネルギーvE-40が60Jを超えており、-40℃の温度域においても十分な靱性が得られることがわかる。
本出願は、2015年6月5日出願の日本特許出願(特願2015-115277)、2016年2月9日出願の日本特許出願(特願2016-023186)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。
A1~A8 直線
B 直径0.40μmの真円
C 円相当直径が0.40μm以上の炭化物
D 円相当直径が0.40μm未満の炭化物
Claims (3)
- C:0.02質量%以上0.08質量%以下、
Si:0.10質量%以上0.30質量%以下、
Mn:1.20質量%以上2.0質量%以下、
Ni:0.50質量%以上3.00質量%以下、
Cr:0質量%以上0.70質量%以下、
Mo:0.10質量%以上0.70質量%以下、
Ti:0.04質量%以上0.08質量%以下、
B:0.0010質量%以上0.0050質量%以下、
O:0.030質量%以上0.100質量%以下、
N:0質量%超0.015質量%以下、
Nb+V:0.008質量%以上0.05質量%以下、並びに
残部:Fe及び不可避的不純物
である組成を有し、
円相当直径が0.40μm未満の炭化物の平均円相当直径が0.10μm以上であり、粒界に存在し、円相当直径が0.40μm以上の炭化物の平均円相当直径が0.75μm以下である溶接金属。 - Cu:0質量%超1.0質量%以下、
Co:0質量%超1.0質量%以下、及び
Al:0質量%超0.030質量%以下
からなる群より選択される少なくとも1種の組成をさらに含む請求項1に記載の溶接金属。 - 請求項1又は請求項2に記載の溶接金属を有する溶接構造体。
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CN201680032091.4A CN107614189A (zh) | 2015-06-05 | 2016-06-02 | 焊接金属和焊接结构体 |
US15/579,483 US20180147674A1 (en) | 2015-06-05 | 2016-06-02 | Welded metal and welded structure |
KR1020177034938A KR20180002791A (ko) | 2015-06-05 | 2016-06-02 | 용접 금속 및 용접 구조체 |
EP16803462.7A EP3305463A4 (en) | 2015-06-05 | 2016-06-02 | Welded metal and welded structure |
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JP2016023186A JP2017001094A (ja) | 2015-06-05 | 2016-02-09 | 溶接金属及び溶接構造体 |
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WO2016195028A1 true WO2016195028A1 (ja) | 2016-12-08 |
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CN110434507A (zh) * | 2019-08-22 | 2019-11-12 | 华南理工大学 | 一种用于海洋工程的水下增材修复金属丝材 |
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JP2008068274A (ja) * | 2006-09-12 | 2008-03-27 | Kobe Steel Ltd | 低温靭性に優れた高強度溶接金属 |
WO2014104731A1 (ko) * | 2012-12-27 | 2014-07-03 | 주식회사 포스코 | 충격인성이 우수한 초고강도 플럭스 코어드 아크 용접이음부 및 이를 제조하기 위한 용접 와이어 |
JP2014195832A (ja) * | 2013-03-08 | 2014-10-16 | 株式会社神戸製鋼所 | 溶接金属 |
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JP2008068274A (ja) * | 2006-09-12 | 2008-03-27 | Kobe Steel Ltd | 低温靭性に優れた高強度溶接金属 |
WO2014104731A1 (ko) * | 2012-12-27 | 2014-07-03 | 주식회사 포스코 | 충격인성이 우수한 초고강도 플럭스 코어드 아크 용접이음부 및 이를 제조하기 위한 용접 와이어 |
JP2014195832A (ja) * | 2013-03-08 | 2014-10-16 | 株式会社神戸製鋼所 | 溶接金属 |
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Publication number | Priority date | Publication date | Assignee | Title |
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CN110434507A (zh) * | 2019-08-22 | 2019-11-12 | 华南理工大学 | 一种用于海洋工程的水下增材修复金属丝材 |
CN110434507B (zh) * | 2019-08-22 | 2021-11-09 | 华南理工大学 | 一种用于海洋工程的水下增材修复金属丝材 |
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