WO2011068216A1 - 高エネルギー密度ビームを用いた突合せ溶接継手 - Google Patents
高エネルギー密度ビームを用いた突合せ溶接継手 Download PDFInfo
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- WO2011068216A1 WO2011068216A1 PCT/JP2010/071721 JP2010071721W WO2011068216A1 WO 2011068216 A1 WO2011068216 A1 WO 2011068216A1 JP 2010071721 W JP2010071721 W JP 2010071721W WO 2011068216 A1 WO2011068216 A1 WO 2011068216A1
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K15/00—Electron-beam welding or cutting
- B23K15/0046—Welding
- B23K15/0053—Seam welding
- B23K15/006—Seam welding of rectilinear seams
-
- 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
- B23K15/00—Electron-beam welding or cutting
- B23K15/0046—Welding
- B23K15/0053—Seam welding
- B23K15/0073—Seam welding with interposition of particular material to facilitate connecting the parts, e.g. using a filler
-
- 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
- B23K15/00—Electron-beam welding or cutting
- B23K15/06—Electron-beam welding or cutting within a vacuum chamber
-
- 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
- B23K26/00—Working by laser beam, e.g. welding, cutting or boring
- B23K26/20—Bonding
- B23K26/21—Bonding by welding
- B23K26/211—Bonding by welding with interposition of special material to facilitate connection of the parts
-
- 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
- B23K26/00—Working by laser beam, e.g. welding, cutting or boring
- B23K26/20—Bonding
- B23K26/21—Bonding by welding
- B23K26/24—Seam welding
- B23K26/26—Seam welding of rectilinear seams
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F03—MACHINES OR ENGINES FOR LIQUIDS; WIND, SPRING, OR WEIGHT MOTORS; PRODUCING MECHANICAL POWER OR A REACTIVE PROPULSIVE THRUST, NOT OTHERWISE PROVIDED FOR
- F03D—WIND MOTORS
- F03D13/00—Assembly, mounting or commissioning of wind motors; Arrangements specially adapted for transporting wind motor components
- F03D13/10—Assembly of wind motors; Arrangements for erecting wind motors
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/04—Tubular or hollow articles
- B23K2101/06—Tubes
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2101/00—Articles made by soldering, welding or cutting
- B23K2101/18—Sheet panels
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K2103/00—Materials to be soldered, welded or cut
- B23K2103/02—Iron or ferrous alloys
- B23K2103/04—Steel or steel alloys
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F05—INDEXING SCHEMES RELATING TO ENGINES OR PUMPS IN VARIOUS SUBCLASSES OF CLASSES F01-F04
- F05B—INDEXING SCHEME RELATING TO WIND, SPRING, WEIGHT, INERTIA OR LIKE MOTORS, TO MACHINES OR ENGINES FOR LIQUIDS COVERED BY SUBCLASSES F03B, F03D AND F03G
- F05B2230/00—Manufacture
- F05B2230/20—Manufacture essentially without removing material
- F05B2230/23—Manufacture essentially without removing material by permanently joining parts together
- F05B2230/232—Manufacture essentially without removing material by permanently joining parts together by welding
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E10/00—Energy generation through renewable energy sources
- Y02E10/70—Wind energy
- Y02E10/72—Wind turbines with rotation axis in wind direction
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E10/00—Energy generation through renewable energy sources
- Y02E10/70—Wind energy
- Y02E10/728—Onshore wind turbines
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P70/00—Climate change mitigation technologies in the production process for final industrial or consumer products
- Y02P70/50—Manufacturing or production processes characterised by the final manufactured product
Definitions
- the present invention relates to a welded joint that is butt welded by irradiating a pair of steel materials with a high energy density beam.
- the present invention relates to a welded joint having excellent fatigue characteristics in a vibration environment in the gigacycle range.
- a tube having a large cross section with a plate thickness of 50 mm or more, for example, about 100 mm, and a diameter of about 4 m is provided at the foundation of the wind power generation tower.
- the structure is adopted, and the total height of the tower is 80 m or more. It is required to weld and assemble such a huge structure easily and efficiently on the coast near the construction site.
- high energy density beam welding such as electron beam welding and laser beam welding is a welding method capable of efficient welding.
- electron beam welding since it is necessary to perform welding while maintaining a high vacuum state in a vacuum chamber, conventionally, the size of the steel plate that can be welded is limited.
- RPEBW Reduced Pressured Electron Beam Welding
- a molten metal portion (hereinafter referred to as a weld metal) that is melted by an electron beam and then solidified in order to perform welding in a state where the degree of vacuum is lowered as compared with a method of welding in a vacuum chamber.
- a weld metal a molten metal portion that is melted by an electron beam and then solidified in order to perform welding in a state where the degree of vacuum is lowered as compared with a method of welding in a vacuum chamber.
- a weld metal is used in which the Ni content of the weld metal is 0.1 to 4.5% by mass by attaching a plate-like insert metal such as Ni to the weld surface and performing electron beam welding.
- a method for improving toughness such as Charpy impact value is proposed in Patent Document 6 and Patent Document 7.
- the offshore wind power generation tower is constantly exposed to vibrations caused by strong wind as described above, the structure of the foundation is constantly subjected to repeated loads, and the welds are constantly subjected to repeated stresses. For this reason, the welded portion of the above structure is required to have fatigue resistance against vibrations in the gigacycle region (10 9 to 10 ) whose order is different from the normal fatigue cycle (10 6 to 7 ).
- the weld metal in the weld zone shrinks near room temperature in the final stage of welding, so that tensile residual stress is induced.
- the fatigue strength may be significantly reduced due to the stress ratio effect. Therefore, there is a concern that fatigue cracks may occur due to tensile residual stress with respect to vibration in the gigacycle region.
- An object of the present invention is to provide a welded joint having fatigue characteristics that can withstand vibrations in the gigacycle range and sufficient fracture toughness.
- a weld joint according to an aspect of the present invention includes a pair of steel materials; and a weld metal formed by welding with a high energy density beam at a butt weld between the steel materials.
- the transformation start temperature Ms calculated by the following mathematical formula (a) using the composition by mass% is 250 ° C. or lower.
- Ms (° C.) 371-353C-22Si-24.3Mn—7.7Cu-17.3Ni-17.7Cr-25.8Mo (a)
- the composition of the weld metal preferably includes Ni: 0.5 to 4.0% by mass and Cr: 0.5 to 6.0% by mass. .
- the composition of the weld metal is one or two of Mo: 0.1 to 2.0% by mass and Cu: 0.1 to 5.0% by mass. It is preferable to contain seeds; Ni, Cr, Mo, and Cu in a total amount of 1.1 to 10.0% by mass; (4)
- the composition of the weld metal preferably contains Ni: 4.0 to 6.0% by mass.
- the composition of the weld metal is Cr: 0.1 to 6.0 mass%, Mo: 0.1 to 2.0 mass%, and Cu: 0.00. It is preferable to contain 1 to 5.0% by mass of one or more; and to contain Ni, Cr, Mo and Cu in a total of 4.1 to 10.0% by mass; (6)
- hardenability index D I of the weld metal is calculated by the following equation (b) using a mass% of the composition of the weld metal, 0.1 or higher It is preferable that it is 3.0 or less.
- the composition of the steel material is C: 0.01 to 0.08 mass%, Si: 0.05 to 0.80 mass%, Mn: 0.8 to 2.5% by mass, P ⁇ 0.03% by mass, S ⁇ 0.02% by mass, Al ⁇ 0.008% by mass, Ti: 0.005 to 0.030% by mass; balance Preferably iron and unavoidable impurities;
- the composition of the steel material is Cu: 0.1 to 1.0 mass%, Ni: 0.1 to 6.0 mass%, Cr: 0.1 to 1.0% by mass, Mo: 0.1-0.5% by mass, Nb: 0.01-0.08% by mass, V: 0.01-0.10% by mass, B: 0.0005-0.
- the thickness of the steel material is preferably 30 mm or more and 200 mm or less.
- the high energy density beam is preferably an electron beam.
- the transformation start temperature of the weld metal as a welding condition that causes compressive residual stress instead of tensile residual stress in a welded portion in welding using a high energy density beam such as an electron beam.
- a high energy density beam such as an electron beam.
- a high-strength steel sheet particularly a steel sheet having a thickness of 30 mm or more
- a high energy density beam is irradiated with a high energy density beam and welded into a butt weld joint
- it has fatigue resistance in a vibration environment in the gigacycle range, and A weld joint having a sufficiently high fracture toughness value can be formed.
- a high energy density beam welded joint (hereinafter referred to as a welded joint) 10 will be described with reference to FIG. 1B.
- the welded joint 10 is welded using a high energy density beam, and an electron beam is used as the high energy density beam in this embodiment.
- an electron beam is used as the high energy density beam in this embodiment.
- RPEBW Reduced Pressure Electron Beam Welding
- the welded joint 10 includes a pair of steel materials (welding base metal) 1 and a weld metal 4 formed by welding to the butt weld 6 between the steel materials 1 by an electron beam.
- the martensitic transformation start temperature Ms (° C.) calculated by the following formula (a) using (mass%) is 250 ° C. or less.
- Ms 371-353C-22Si-24.3Mn-7.7Cu-17.3Ni-17.7Cr-25.8Mo (a)
- the inventors have found that the transformation start temperature is overestimated in a generally known equation for estimating the martensite transformation start temperature because the cooling rate of the welded portion 6 in the welded joint 10 is large. Therefore, the formula for estimating the general transformation start temperature was corrected, and the formula (a) was derived.
- the martensitic transformation end temperature (Mf (° C.)) is preferably room temperature. In general, the transformation that starts transformation at 250 ° C.
- the temperature calculated by the numerical value (a) may simply be 250 ° C. or less.
- Ms is simply referred to as a transformation start temperature.
- FIG. 1A shows a conceptual diagram of a high energy density beam welding method.
- an insert metal 3 is inserted between a groove 2 between a pair of steel materials 1, and the insert metal 3 and the surface of the groove 2 of the pair of steel materials 1 are welded by a high energy density beam. To do.
- the transformation of the weld metal 4 starts at a relatively low temperature, that is, 250 ° C. or lower, in the process of cooling the weld metal 4 to room temperature. . Due to the transformation expansion of the weld metal 4, the compressive stress 5 generated in the welded portion 6 is maintained up to room temperature. Thereby, the fatigue strength of the welded joint 10 can be improved.
- the components of the insert metal 3 and the steel material are adjusted so that the transformation start temperature Ms of the weld metal 4 formed in the welded portion 6 of the weld joint 10 is 250 ° C. or less. .
- the width of the weld metal can be predicted in advance from the welding conditions, etc., the component of the weld metal 3 and the component and size of the steel material 1 are adjusted to the target component of the weld metal. That is, it is easy to adjust the transformation start temperature Ms of the weld metal 4.
- the weld joint 10 has a transformation start temperature of 250 ° C. or lower, so the weld metal 4 undergoes martensitic transformation in a state of being restrained from the steel material 1. At this time, since the weld metal 4 is going to expand, the compressive residual stress is applied from the steel material 1. As a result, the fatigue characteristics of the welded joint 10 are improved to fatigue resistance that can withstand even in a vibration environment in the gigacycle range. Furthermore, since the hardenability of the weld metal is improved, the weld joint 10 having a fine structure and sufficient fracture toughness can be provided.
- the steel material 1 used for the welded joint 10 of the present embodiment is not particularly limited, it is preferable to use a steel material having a plate thickness of 30 mm or more or 50 mm or more, in which the above-described problem becomes significant. Moreover, it is preferable that the upper limit of plate
- the steel material 1 to be used is not particularly limited, but is preferably a steel material in which C is limited to 0.2% by mass or less, and the yield strength is 355 MPa or more.
- the tensile strength may be limited to 690 MPa or less or 780 MPa or less.
- Such a high-strength steel plate may be a steel plate manufactured from a structural steel for welding having a known component composition.
- the composition of the steel material 1 is not particularly limited. For example, in mass%, C: 0.01 to 0.08%, Si: 0.05 to 0.80%, Mn: 0.8 to 2.5 %, P: 0.03% or less, S: 0.02% or less, Al: 0.008% or less, Ti: 0.005 to 0.030%; balance iron and steel composition which is an inevitable impurity Is preferred. And, with this composition as a basic component, Cr, Mo, Ni, Cu, W, Co, V, Nb, Ti, Zr depending on required properties such as improvement of the strength of the base material (steel material 1) and joint toughness.
- Ta, Hf, REM, Y, Ca, Mg, Te, Se, and steel containing one or more of them in a total of 8% or less can be used.
- Specific examples include, by mass, Cu: 0.1 to 1.0%, Ni: 0.1 to 6.0%, Cr: 0.1 to 1.0%, Mo: 0.1 to 0 .6%, Nb: 0.01 to 0.08%, V: 0.01 to 0.10%, B: 0.0005 to 0.0050% of one or more steel compositions It is preferable.
- these alloy components are contained in the steel material 1, the steel material price becomes very expensive. In practice, a much cheaper welded joint can be obtained by welding using an insert material containing an expensive alloy component. For this reason, you may restrict
- steel containing 4% or less, 2% or less, or 1% or less in total of one or more of Ni, Cr, Mo, and Cu may be used.
- one or more of Cr, Mo, Ni, Cu, W, Co, V, Nb, Ti, Zr, Ta, Hf, REM, Y, Ca, Mg, Te, Se, and B are totaled.
- Steels containing up to 4% or 2% may be used.
- the amount of C contained in the steel material 1 is preferably set to 0.01% or more. If necessary, the amount of C contained in the steel material 1 may be limited to 0.02% or more or 0.03% or more. In order to prevent a decrease in toughness due to abnormal hardening of the weld metal 4, the C content may be limited to 0.12% or less. If necessary, the amount of C contained in the steel material 1 may be limited to 0.08% or less or 0.06% or less. In order to obtain good toughness with the weld metal 4, the amount of Si contained in the steel material 1 is preferably 0.80% or less.
- the amount of Si contained in the steel material 1 may be limited to 0.50% or less, 0.30% or less, or 0.15% or less.
- the lower limit of the Si content is not particularly required, but is preferably 0.05% or more for appropriate deoxidation treatment. If necessary, the Si content may be limited to 0.08% or more.
- Mn is an inexpensive element that has a great effect of optimizing the microstructure. In order to ensure the strength and toughness required for structural steel, it is preferable to add 0.8 to 2.5% of Mn to the steel material 1. In order to prevent abnormal hardening of the weld metal 4, the upper limit of the amount of Mn contained in the steel material 1 may be limited to 2.3%, 2.0%, or 1.9%.
- P and S are inevitable impurities, but are preferably limited to 0.03% or less and 0.02% or less, respectively, in order to deteriorate toughness and the like.
- the upper limit of the amount of P contained in the steel material 1 is limited to 0.02%, 0.015% or 0.010%, and the upper limit of the amount of S is 0. It may be limited to .015%, 0.010% or 0.006%.
- the Al content of the steel material 1 is desirably 0.008% or less.
- the upper limit of the Al content may be limited to 0.006%, 0.005%, or 0.003%.
- the amount of Ti contained in the steel material 1 is desirably 0.005 to 0.030%. If necessary, the upper limit of the Ti content may be limited to 0.025%, 0.020%, or 0.015%. Further, the lower limit of the Ti content may be limited to 0.007% or 0.009%.
- Cu is an element that improves the strength and toughness of the steel material 1 and may be added as necessary. In order to improve strength and toughness, 0.1% or more or 0.3% or more of Cu may be added.
- the upper limit of the Cu content is preferably set to 1.0% in order to prevent wrinkling of the steel material 1 due to the addition of a large amount of Cu. You may restrict
- Ni is an element useful for improving the toughness of the steel material 1 and the weld metal 4, and the amount of Ni may be added to the steel material 1 by 0.1% or more. On the other hand, since Ni is expensive, it is desirable to make it 6.0% or less. In order to reduce the price of the steel material 1, the upper limit of the Ni content may be limited to 2.0%, 1.0%, or 0.5%.
- Mo is an element effective for improving the strength. If necessary, the amount of Mo may be added to the steel material 1 by 0.1% or more.
- the weld metal 4 is abnormally hardened and the toughness is lowered. If necessary, the amount of Mo contained in the steel material 1 may be limited to 0.2% or less or 0.15% or less.
- Nb is an element effective for improving the strength and toughness of the steel material 1, and if necessary, the amount of Nb may be added to the steel material 1 by 0.01% or more. If added in a large amount, the toughness of the weld metal 4 decreases, so the Nb content is preferably 0.08% or less. If necessary, the Nb content may be limited to 0.05% or less or 0.03% or less.
- V is an element effective for improving the strength of the steel material 1, and 0.01% or more may be added as necessary.
- the V content is preferably 0.10% or less. If necessary, the V content may be limited to 0.07% or less or 0.04% or less.
- B is an element effective for improving the strength of the steel material 1. If necessary, the amount of B may be added to the steel material 1 by 0.0005% or more. If added in a large amount, the toughness of the weld metal 4 decreases, so the B content is preferably 0.0050% or less. If necessary, the B content may be limited to 0.0020% or less or 0.0015% or less.
- Ca and REM are effective elements for improving lamellar tear resistance, and 0.0005% or more of Ca and REM may be added to the steel material 1 as necessary.
- Mg is effective in improving the toughness of the weld heat affected zone of the steel material 1 and may be added by 0.0003% or more.
- the toughness of the steel material decreases, so the Mg content is preferably 0.0050% or less.
- the composition of the weld metal 4 preferably contains, for example, Ni: 0.5 to 4.0% and Cr: 0.5 to 6.0%. Thereby, it becomes easy to make the transformation start temperature Ms 250 degrees C or less. In addition, by suppressing the expensive Ni content, the welded joint 10 with improved fatigue strength can be obtained at low cost. In this case, it further contains one or two of Mo: 0.1 to 2.0% and Cu: 0.1 to 5.0% by mass; Ni, Cr, Mo and Cu in total Preferably, the steel composition contains 1.1 to 10.0%. Thus, by including one or two of Mo and Cu, the fatigue strength can be improved and sufficient fracture toughness can be obtained. Alternatively, the composition of the weld metal 4 may contain, for example, Ni: 4.0 to 6.0% in addition to the above.
- Ni is an effective element for lowering the transformation start temperature Ms of the weld metal 4 and improving the fatigue strength of the welded joint 10. Further, it is an element that improves joint characteristics such as strength and toughness.
- the lower limit of the Ni content is preferably set to 0.5% as a minimum at which the effect of improving fatigue strength can be sufficiently expected. In order to surely improve the fatigue strength, it is more desirable to set the lower limit of the Ni content to 1.0% or 2.0%.
- the Ni content of the weld metal exceeds 6.0%, the weld metal 4 may not be transformed into bainite or martensite that transforms at a low temperature, and cooling may be completed as austenite, improving fatigue strength. Cannot be expected. Thereby, it is preferable to make the upper limit of Ni content 6.0%.
- Cr and Mo are elements that reduce the transformation start temperature Ms of the weld metal 4, improve the strength, and ensure hardenability.
- Cr and Mo are more effective in improving the strength of the weld metal 4 and ensuring hardenability than Ni.
- the content of Cr and Mo is 0.1% or more. It is preferable that On the other hand, since Cr and Mo are less effective in improving the toughness of the weld metal 4 than Ni, if excessively contained, the toughness of the weld metal 4 may be lowered.
- the upper limit of the Cr content is 6 0.0% and the upper limit of the Mo content is preferably 2.0%.
- the lower limit of the Cr content is limited to 1.5% or 2%, and when the Ni content is 1.0% or less, the lower limit of the Cr content is It may be limited to 2.0% or 2.5%.
- the lower limit of the Cr content may be limited to 4.0% or 3.0%.
- the lower limit of the Mo content may be limited to 1%, 0.5%, or 0.2%. If necessary, even when the Ni content exceeds 4.0%, the lower limit of the Cr content may be limited to 0.5%.
- Cu is an element that has the effect of reducing the transformation start temperature Ms of the weld metal 4, improving the strength, and ensuring hardenability.
- Cu preferably has a Cu content lower limit of 0.1%.
- the upper limit of the Cu content is preferably 5.0%. More preferably, the upper limit of the Cu content is 0.3%.
- the weld metal 4 of the present invention can further contain component elements in the following content ranges for the following purposes.
- B is an element that dramatically improves the hardenability, and ensures the hardenability of the weld metal 4 and makes the microstructure of the weld metal 4 stronger. In addition, it has the effect of suppressing the formation of a structure that starts transformation at a high temperature and making it a microstructure that transforms at a lower temperature.
- B since the weld metal 4 has a higher oxygen content than the steel material 1, B may be combined with oxygen and deprived of the above-described effects.
- the amount of oxygen and nitrogen are extremely small, so even to improve the above-described hardenability by B in the weld metal and the tensile strength and fatigue strength by microstructure control.
- the lower limit of the B content is 0.0003%.
- the upper limit of the B addition amount is preferably 0.005% because the effect obtained by adding B does not increase much even if an amount exceeding 0.0003% is added.
- Nb, V, and Ti are all elements that have the function of forming carbides in the weld metal 4 to increase the strength, and contain a small amount of one or more of Nb, V, and Ti in the weld metal 4.
- the joint strength can be improved. If the lower limit of the total content of one or more of Nb, V, and Ti is less than 0.005%, improvement in joint strength cannot be expected so much, so the lower limit of the total content is 0.005%. Is preferable. On the other hand, if the total content exceeds 0.3%, the strength of the weld metal 4 becomes excessive, and problems occur in the joint characteristics. Therefore, the total content upper limit is preferably set to 0.3%.
- the lower limit of the Ti content is preferably 0.003%. Is desirable.
- the lower limit of the Al content may be limited to 0.003%, 0.005%, or 0.008%.
- the component of the insert metal 3 and the thickness thereof may be selected so as to be the target component of the weld metal 4.
- the insert metal 3 pure Ni or Ni: 1 to 10%, Cr: 0.1 to 2.0%, Mo: 0.1 to 2.0%, and Cu: 0.1 to 5.
- a metal foil containing 0.5% to 10.0% in total of 1% or 2% of 0% can be used.
- the hardness of the weld metal 4 is preferably within 140% of the hardness of the steel material 1 as the base material.
- the weld metal 4 is preferably martensitic in order to lower the transformation start temperature Ms so that the expansion amount during transformation of the weld metal 4 can be utilized at room temperature.
- the structure of the weld metal 4 is too hard, it causes a decrease in the fracture toughness value ⁇ c due to an increase in local stress. Therefore, it is preferably suppressed to 140% or less.
- the composition of the weld metal 4 is Ni: 0.5-6.0%, Cr: 0.1-6.0%, Mo: 0.1-2.0%, and Cu: 0.1-5.0%
- the steel material 1 and the insert metal that satisfy the condition of containing 0.5 to 10.0%, preferably 1.1 to 10.0% in total, of one or more of It is preferable to appropriately adjust the balance between components with the weld metal 4 formed using 3 and to adjust the cooling rate after welding. Thereby, since the hardness of the weld metal 4 can be prevented from becoming too high, the hardness difference between the weld metal 4 and the steel material 1 (the hardness of the weld metal 4 is within 140% of the hardness of the steel material 1). Can be adjusted.
- the total content of Ni, Cr, Mo and Cu in the weld metal 4 is 0.5% or more, 1.0%, 2. You may restrict
- the hardenability index D of the weld metal 4 calculated by the following mathematical formula (b) using the composition of the weld metal 4 is used. I is preferably 0.1 or more and 3.0 or less.
- hardenability index D I 0.36 ⁇ C (1 + 0.7Si) (1 + 3.33Mn) (1 + 0.35Cu) (1 + 0.36Ni) (1 + 2.16Cr) (1 + 3Mo) (b)
- hardenability index D I is preferably 3.0 or less. If necessary, it may limit the upper limit of D I value 1.2,0.9 or 0.7.
- the hardenability index D I value is too low, and since they are not a martensite structure, it is preferable that the D I value of 0.1 or more.
- D I value lower limit of 0.2 or more may be limited to 0.25 or more, or 0.3 or more.
- the welding conditions using a high energy density beam are not particularly limited.
- the voltage is 175 V
- the current is 120 mA
- the welding speed is about 125 mm / min. Done on condition.
- Electron beam welding is usually performed under a high vacuum of 10 to 3 mbar or less, but is a welded joint welded under a low vacuum such as the RPEBW method described above, for example, under a vacuum of about 1 mbar. Also, this embodiment can be applied.
- the electron beam irradiation area becomes large during electron beam welding, the amount of heat input to the steel material 1 becomes excessive, and the structure of the FL part (Fusion Line, the boundary part between the steel material 1 and the weld metal 4) becomes coarse. It is not preferable for stably securing the fracture toughness value ⁇ c of the FL portion.
- the width of the weld metal tends to increase compared to a welded joint produced by electron beam welding (EBW welding) in a high vacuum state in a vacuum chamber. .
- EBW welding electron beam welding
- the width w of the weld metal 4 shown in FIG. It is preferable to make it 20% or less or 10% or less of the plate thickness t of 1.
- the electron beam is used as the high energy density beam because it is suitable for the local rapid heating and rapid cooling of the welded portion 6, the present invention is not limited to this.
- the present invention will be described based on examples, but the conditions in the examples are one condition example adopted to confirm the feasibility and effects of the present invention, and the present invention is an example of this one condition. It is not limited to. That is, the present invention can employ various conditions or combinations of conditions as long as the object of the present invention is achieved without departing from the gist of the present invention.
- a fatigue test was performed at an axial force, a stress ratio of 0.1, and a repetition rate of 5 Hz, and a fatigue strength of 2 ⁇ 10 6 times was obtained. Furthermore, the ultrasonic test piece 24 was sampled in the welded joint of FIG. 2, and 2 ⁇ 10 6 fatigue strengths and 2 ⁇ 10 9 gigacycle fatigue strengths were obtained, and the reduction ratio was determined. The fatigue strength (estimated value) under the gigacycle was evaluated by multiplying the fatigue strength of 2 ⁇ 10 6 times obtained in the joint fatigue test by the reduction ratio. The results are shown in Tables 4 and 5 together with the welding conditions.
- the fracture toughness value ⁇ c (mm) is a value obtained at a test temperature of ⁇ 10 ° C. in a CTOD (Crack Tip Opening Displacement) test.
- the CTOD test is one of tests for evaluating the fracture toughness of a structure in which a defect exists. In this example, the average value of three welded joints was obtained.
- Joint tensile strength is the result of the joint tensile test conducted by preparing the U.S. Maritime Association (NK) Steel Ship Rules / Inspection Guidelines (K knitted material) No. 1 test piece. Yes, it shows the strength at which it breaks.
- joint no. In 2, 6, 8, 10 and 12 since the transformation start temperature exceeds 250 ° C., there is a tensile residual stress in the weld in the weld metal 4 and the fatigue strength is 2 ⁇ 10 6 times under the gigacycle. It can be seen that the joint fatigue strength at is significantly reduced.
- the joint No. In 1, 3, 4, 5, 7, 9, 11, 13 to 20 the welded portion undergoes transformation at a temperature of 250 ° C. or less, and the compressive residual stress is acting. Therefore, fatigue strength of 2 ⁇ 10 6 times All are over 260 MPa, and the joint fatigue strength under the gigacycle is over 200 MPa. Therefore, the joint No. In 1, 3, 4, 5, 7, 9, 11, 13 to 20, it can be seen that the joint fatigue strength under the gigacycle is not greatly reduced.
- a high-strength steel plate when welded with a high energy density beam to form a welded structure, it has a fatigue resistance property in a vibration environment in the gigacycle region and has a sufficiently high fracture toughness value ⁇ c.
- a joint can be formed, and industrial applicability is high as a base member of an offshore wind power generation tower.
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Abstract
Description
本願は、2009年12月04日に、日本に出願された特願2009-277035号に基づき優先権を主張し、その内容をここに援用する。
すなわち、
(1)本発明の一態様に係る溶接継手では、一対の鋼材と;前記鋼材間の突合せ溶接部に、高エネルギー密度ビームにより溶接されて形成された溶接金属と;を備え、前記溶接金属の質量%の組成を用いた下記数式(a)により算出される変態開始温度Msが、250℃以下である。
Ms(℃)=371-353C-22Si-24.3Mn-7.7Cu-17.3Ni-17.7Cr-25.8Mo・・・(a)
(3)上記(2)に記載の溶接継手では、前記溶接金属の組成が、Mo:0.1~2.0質量%、およびCu:0.1~5.0質量%の1種または2種を含有し;Ni,Cr,Mo,Cuを合計で1.1~10.0質量%を含有する;ことが好ましい。
(4)上記(1)に記載の溶接継手では、前記溶接金属の組成が、Ni:4.0~6.0質量%を含有することが好ましい。
(5)上記(4)に記載の溶接継手では、前記溶接金属の組成が、Cr:0.1~6.0質量%、Mo:0.1~2.0質量%、およびCu:0.1~5.0質量%の1種または2種以上を含有し;Ni,Cr,Mo,Cuを合計で4.1~10.0質量%を含有する;ことが好ましい。
(6)上記(5)に記載の溶接継手では、前記溶接金属の質量%の組成を用いた下記数式(b)により算出される前記溶接金属の焼入性指数DIが、0.1以上3.0以下であることが好ましい。
DI =0.36√C(1+0.7Si)(1+3.33Mn)(1+0.35Cu)(1+0.36Ni)(1+2.16Cr)(1+3Mo)・・・(b)
(7)上記(1)~(5)に記載の溶接継手では、前記鋼材の組成が、C:0.01~0.08質量%、Si:0.05~0.80質量%、Mn:0.8~2.5質量%、P≦0.03質量%、S≦0.02質量%、Al≦0.008質量%、Ti:0.005~0.030質量%を含有し;残部鉄および不可避的不純物である;ことが好ましい。
(8)上記(7)に記載の溶接継手では、前記鋼材の組成が、Cu:0.1~1.0質量%、Ni:0.1~6.0質量%、Cr:0.1~1.0質量%、Mo:0.1~0.5質量%、Nb:0.01~0.08質量%、V:0.01~0.10質量%、B:0.0005~0.0050質量%の1種または2種以上を含有することが好ましい。
(9)上記(1)~(5)に記載の溶接継手では、前記鋼材の厚みが30mm以上200mm以下であることが好ましい。
(10)上記(1)~(5)に記載の溶接継手では、前記高エネルギー密度ビームが電子ビームであることが好ましい。
さらには、高強度鋼板、特に板厚が30mm以上の鋼板に高エネルギー密度ビームを照射し、溶接して突合せ溶接継手とする際、ギガサイクル域の振動環境における耐疲労特性を有し、かつ、破壊靱性値が十分に高い溶接継手を形成することができる。
溶接継手10は、一対の鋼材(溶接母材)1と、鋼材1間の突合せ溶接部6に、電子ビームにより溶接され形成された溶接金属4と、を備えており、溶接金属4の組成(質量%)を用いた下記数式(a)により算出されるマルテンサイト変態開始温度Ms(℃)が、250℃以下である。
Ms=371-353C-22Si-24.3Mn-7.7Cu-17.3Ni-17.7Cr-25.8Mo・・・(a)
発明者らは、溶接継手10における溶接部6の冷却速度が大きいため、一般に知られているマルテンサイト変態開始温度を推定する式では、変態開始温度を過大評価してしまうことをつきとめた。そこで、一般の変態開始温度を推定する式を補正し、数式(a)を導いた。
また、マルテンサイト変態終了温度(Mf(℃))は室温であることが望ましい。
なお、一般的に250℃以下で変態開始する変態は、マルテンサイト変態である。しかし、本発明においては厳密に250℃以下でマルテンサイト変態が開始することを確認する必要はなく、250℃以下で体積膨張する変態を開始すればよい。そこで、本発明においては、数値(a)で算出された温度が単に250℃以下であればよい。また、以下では、Msを単に変態開始温度と記す。
図1Aには、高エネルギー密度ビームの溶接方法の概念図が示されている。図1Aに示されるように、一対の鋼材1間の開先2の間にインサートメタル3を装入し、高エネルギー密度ビームによりインサートメタル3と一対の鋼材1の開先2の表面とを溶接する。
また、本実施形態の溶接継手10に用いられる鋼板1の組成は、使用するインサートメタル3の組成との組み合わせによって、形成される溶接金属4の変態開始温度が250℃以下となるように調整されている。使用する鋼材1は、特に限定されないが、好ましくはCを0.2質量%以下に制限された鋼材であり、降伏強度が355MPa以上である。引張強さを690MPa以下又は780MPa以下に制限してもよい。このような高強度鋼板としては、公知の成分組成の溶接用構造用鋼から製造した鋼板でよい。
構造用の鋼として十分な強度を得るためには、鋼材1に含有されるCの量は0.01%以上とすることが好ましい。必要に応じて、鋼材1に含有されるCの量を0.02%以上または0.03%以上に制限してもよい。溶接金属4の異常な硬化による靭性低下を防止するために、Cの含有量を0.12%以下に制限してもよい。必要に応じて、鋼材1に含有されるCの量を0.08%以下または0.06%以下に制限してもよい。
溶接金属4で良好な靭性を得るためには、鋼材1に含有されるSiの量を0.80%以下とすることが好ましい。必要に応じて、鋼材1に含有されるSiの量を0.50%以下、0.30%以下または0.15%以下に制限してもよい。Siの含有量の下限は特に定める必要はないが、適切な脱酸処理のために0.05%以上とすることが望ましい。必要に応じて、Siの含有量を0.08%以上に制限してもよい。
Mnはミクロ組織を適正化する効果が大きい安価な元素である。構造用の鋼として必要な強度と靭性を確保するために、鋼材1にMnの量を0.8~2.5%添加することが好ましい。溶接金属4の異常硬化を防止するために、鋼材1に含有させるMnの量の上限を2.3%、2.0%または1.9%に制限してもよい。
PおよびSは不可避的不純物であるが、靭性等を劣化させるため、それぞれ0.03%以下および0.02%以下に制限することが好ましい。靭性を改善するためには、低い方が望ましく、鋼材1に含有されるPの量の上限を0.02%、0.015%または0.010%に制限し、Sの量の上限を0.015%、0.010%または0.006%に制限してもよい。
溶接金属4の靭性を高めるため、鋼材1のAlの含有量は0.008%以下とすることが望ましい。靭性の向上のために、Alの含有量の上限を0.006%、0.005%または0.003%に制限してもよい。
溶接金属4の靭性を高めるため、適切な量のTi酸化物を生成させることが好ましい。このために、鋼材1に含有されるTiの量は0.005~0.030%とすることが望ましい。必要に応じて、Tiの含有量の上限を0.025%、0.020%または0.015%に制限してもよい。また、Tiの含有量の下限を0.007%または0.009%に制限してもよい。
Cuは、鋼材1の強度や靭性を向上させる元素であり、必要に応じて添加してよい。強度や靭性を向上させるためには、0.1%以上または0.3%以上のCuを添加してもよい。一方、多量のCu添加による鋼材1の疵等を防止するために、Cu含有量の上限は、1.0%とすることが好ましい。必要に応じて、Cu含有量の上限を0.7%又は0.5%に制限してもよい。
Niは鋼材1および溶接金属4の靭性を向上させるのに有用な元素であり、鋼材1にNiの量を0.1%以上添加してよい。一方、Niは高価であるため、6.0%以下とすることが望ましい。鋼材1の価格を低減させるために、Niの含有量の上限を、2.0%、1.0%または0.5%に制限してもよい。
Moは、強度を向上させるのに有効な元素であり、必要に応じて、鋼材1にMoの量を0.1%以上添加してよい。多量に添加すると溶接金属4が異常に硬化し、靭性が低下するため、0.6%以下とすることが好ましい。必要に応じて、鋼材1に含有されるMoの量を0.2%以下または0.15%以下に制限してもよい。
Nbは、鋼材1の強度や靭性向上に有効な元素であり、必要に応じて、鋼材1にNbの量を0.01%以上添加してよい。多量に添加すると溶接金属4の靭性が低下するため、Nbの含有量は0.08%以下とすることが好ましい。必要に応じて、Nbの含有量を0.05%以下または0.03%以下に制限してもよい。
Vは、鋼材1の強度の向上に有効な元素であり、必要に応じて、0.01%以上を添加してよい。多量に添加すると溶接金属4の靭性が低下するため、Vの含有量は0.10%以下とすることが好ましい。必要に応じて、Vの含有量を0.07%以下または0.04%以下に制限してもよい。
Bは、鋼材1の強度の向上に有効な元素であり、必要に応じて、鋼材1にBの量を0.0005%以上添加してよい。多量に添加すると溶接金属4の靭性が低下するため、Bの含有量は0.0050%以下とすることが好ましい。必要に応じて、Bの含有量を0.0020%以下または0.0015%以下に制限してもよい。
CaおよびREMは、耐ラメラテア特性向上に有効な元素であり、必要に応じて、鋼材1にCaおよびREMの量を0.0005%以上添加してよい。多量に添加すると鋼材1の靭性が低下するため、これらの含有量は0.0050%以下とすることが好ましい。
Mgは、鋼材1の溶接熱影響部の靭性向上に有効であり、0.0003%以上添加してよい。多量に添加すると鋼材の靭性が低下するため、Mgの含有量は0.0050%以下とすることが好ましい。
または、溶接金属4の組成を、上記の他に、例えば、Ni:4.0~6.0%を含有するようにしても良い。この場合、Niの含有量を多くすることにより、靱性を向上させることが可能となる。この場合、さらに、質量で、Cr:0.1~6.0%、Mo:0.1~2.0%、およびCu:0.1~5.0%の1種または2種以上を含有し;Ni,Cr,Mo,Cu合計で4.1~10.0%を含有する鋼組成である;ことが好ましい。このように、Mo,Cuの1種または2種を含有させることにより、疲労強度を向上させ、十分な破壊靱性を得ることが可能となる。
なお、Niの含有量が4.0%以下の場合、溶接金属4の変態開始温度Msを確実に250℃以下とするために、0.5%以上のCrの含有が必要である。Niの含有量が2.0%以下の場合にCrの含有量の下限を1.5%または2%に制限し、Niの含有量が1.0%以下の場合にCr含有量の下限を2.0%または2.5%に制限してもよい。溶接金属4の靭性低下をさけるために、Cr含有量の下限を4.0%または3.0%に制限してもよい。同様な理由により、Moの含有量の下限を1%、0.5%または0.2%に制限してもよい。必要に応じて、Niの含有量が4.0%を超える場合でも、Crの含有量の下限を0.5%に制限してもよい。
また、溶接金属4の変態開始温度Msを確実に低減させるためにも、溶接金属4におけるNi、Cr,MoおよびCuの含有量の合計を、0.5%以上、1.0%、2.0%または3.0%以上に制限してもよい。
また、溶接金属4の異常な硬化を防止して溶接金属4の靭性を向上させるために、溶接金属4の組成を用いた下記数式(b)により算出される溶接金属4の焼入性指数DIが、0.1以上3.0以下であることが好ましい。
DI =0.36√C(1+0.7Si)(1+3.33Mn)(1+0.35Cu)(1+0.36Ni)(1+2.16Cr)(1+3Mo)・・・(b)
溶接金属4の焼入性指数DIが3.0を超えると、溶接金属の硬さが高くなり靭性が低下するため、焼入性指数DIは3.0以下が好ましい。必要に応じて、DI値の上限を1.2、0.9または0.7に制限してもよい。一方、焼入性指数DI値が低過ぎると、マルテンサイト組織とならないため、DI値を0.1以上とすることが望ましい。確実にマルテンサイト組織とするために、DI値の下限を0.2以上、0.25以上または0.3以上に制限してもよい。
本実施形態において、溶接部6の局部的な急速加熱及び急速冷却に適しているため、高エネルギー密度ビームとして電子ビームを用いたが、これに限るものではない。
表中の変態開始温度Ms(℃)は、上述したように、Ms=371-353C-22Si-24.3Mn-7.7Cu-17.3Ni-17.7Cr-25.8Moの数式を用いて求めた。
図2に示される溶接継手内において、継手疲労試験片23を採取し、継手疲労試験片23の裏面23aを機械研削して試験片の表面側から疲労亀裂が発生するように工夫した。軸力、応力比0.1、繰り返し速度5Hzにて疲労試験を行い、2×106回の疲労強度を求めた。さらに、図2の溶接継手内において超音波試験片24を採取し、2×106回の疲労強度、および2×109回までのギガサイクルでの疲労強度を求め、その低下比率をもとめ、継手疲労試験で求めた2×106回の疲労強度にその低下比率をかけて、ギガサイクル下での継手疲労強度(推定値)を評価した。その結果を溶接条件とともに表4、表5に示す。
2 開先
3 インサートメタル
4 溶接金属
5 圧縮応力
6 溶接部
21 鋼板
22 溶接ビード
23 継手疲労試験片
24 超音波疲労試験片
Claims (10)
- 一対の鋼材と;
前記一対の鋼材間の突合せ溶接部に、高エネルギー密度ビームにより溶接されて形成された溶接金属と;を備え、
前記溶接金属の質量%の組成を用いた下記数式(a)により算出される変態開始温度Msが、250℃以下であることを特徴とする溶接継手。
Ms(℃)=371-353C-22Si-24.3Mn-7.7Cu-17.3Ni-17.7Cr-25.8Mo・・・(a) - 前記溶接金属の組成が、Ni:0.5~4.0質量%およびCr:0.5~6.0質量%を含有することを特徴とする請求項1に記載の溶接継手。
- 前記溶接金属の組成が、Mo:0.1~2.0質量%、およびCu:0.1~5.0質量%の1種または2種を含有し;
Ni,Cr,Mo,Cuを合計で1.1~10.0質量%を含有する;
ことを特徴とする請求項2に記載の溶接継手。 - 前記溶接金属の組成が、Ni:4.0~6.0質量%を含有することを特徴とする請求項1に記載の溶接継手。
- 前記溶接金属の組成が、Cr:0.1~6.0質量%、Mo:0.1~2.0質量%、およびCu:0.1~5.0質量%の1種または2種以上を含有し;
Ni,Cr,Mo,Cuを合計で4.1~10.0質量%を含有する;
ことを特徴とする請求項4に記載の溶接継手。 - 前記溶接金属の質量%組成を用いた下記数式(b)により算出される前記溶接金属の焼入性指数DIが、0.1以上3.0以下であることを特徴とする請求項1から請求項5のいずれか1項に記載の溶接継手。
DI =0.36√C(1+0.7Si)(1+3.33Mn)(1+0.35Cu)(1+0.36Ni)(1+2.16Cr)(1+3Mo)・・・(b) - 前記鋼材の組成が、C:0.01~0.08質量%、Si:0.05~0.80質量%、Mn:0.8~2.5質量%、P≦0.03質量%、S≦0.02質量%、Al≦0.008質量%、Ti:0.005~0.030質量%を含有し;
残部鉄および不可避的不純物である;
ことを特徴とする請求項1から請求項5のいずれか1項に記載の溶接継手。 - 前記鋼材の組成が、Cu:0.1~1.0質量%、Ni:0.1~6.0質量%、Cr:0.1~1.0質量%、Mo:0.1~0.5質量%、Nb:0.01~0.08質量%、V:0.01~0.10質量%、B:0.0005~0.0050質量%の1種または2種以上を含有することを特徴とする請求項7に記載の溶接継手。
- 前記鋼材の厚みが30mm以上200mm以下であることを特徴とする請求項1から請求項5のいずれか1項に記載の溶接継手。
- 前記高エネルギー密度ビームが電子ビームであることを特徴とする請求項1から請求項5のいずれか1項に記載の溶接継手。
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MY160917A (en) | 2017-03-31 |
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CN102639277A (zh) | 2012-08-15 |
JP2012102405A (ja) | 2012-05-31 |
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ES2631979T3 (es) | 2017-09-07 |
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CN102639277B (zh) | 2015-08-19 |
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US20120241420A1 (en) | 2012-09-27 |
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