CN109226941B - GMAW (gas metal arc welding) method for low-alloy ultrahigh-strength steel Q1100E thin plate - Google Patents
GMAW (gas metal arc welding) method for low-alloy ultrahigh-strength steel Q1100E thin plate Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 150
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- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 title claims abstract description 21
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- 239000000956 alloy Substances 0.000 title claims abstract description 21
- 239000002184 metal Substances 0.000 title claims description 6
- 229910052751 metal Inorganic materials 0.000 title claims description 6
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 24
- 239000010959 steel Substances 0.000 claims abstract description 24
- 230000002787 reinforcement Effects 0.000 claims abstract description 10
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- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 claims abstract description 4
- 230000008030 elimination Effects 0.000 claims abstract description 4
- 238000003379 elimination reaction Methods 0.000 claims abstract description 4
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- 238000012360 testing method Methods 0.000 claims description 16
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- CURLTUGMZLYLDI-UHFFFAOYSA-N Carbon dioxide Chemical compound O=C=O CURLTUGMZLYLDI-UHFFFAOYSA-N 0.000 claims description 12
- 239000007789 gas Substances 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 9
- 238000005498 polishing Methods 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 7
- 210000001503 joint Anatomy 0.000 claims description 7
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 229910002092 carbon dioxide Inorganic materials 0.000 claims description 6
- 239000001569 carbon dioxide Substances 0.000 claims description 6
- 238000004140 cleaning Methods 0.000 claims description 6
- 238000000227 grinding Methods 0.000 claims description 6
- 239000000126 substance Substances 0.000 claims description 5
- JEIPFZHSYJVQDO-UHFFFAOYSA-N iron(III) oxide Inorganic materials O=[Fe]O[Fe]=O JEIPFZHSYJVQDO-UHFFFAOYSA-N 0.000 claims description 3
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- VZSRBBMJRBPUNF-UHFFFAOYSA-N 2-(2,3-dihydro-1H-inden-2-ylamino)-N-[3-oxo-3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)propyl]pyrimidine-5-carboxamide Chemical compound C1C(CC2=CC=CC=C12)NC1=NC=C(C=N1)C(=O)NCCC(N1CC2=C(CC1)NN=N2)=O VZSRBBMJRBPUNF-UHFFFAOYSA-N 0.000 description 2
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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
- B23K9/16—Arc welding or cutting making use of shielding gas
- B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
-
- 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
- B23K9/235—Preliminary treatment
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
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Abstract
A GMAW welding method for low-alloy ultrahigh-strength steel Q1100E thin plates, wherein the thickness of steel plates is 8-12 mm, and the steel plates are butted by adopting the same plate thickness combination, comprises the following steps: processing a V-shaped groove; pre-treating; strictly controlling the preheating temperature, the interlayer temperature and the heat input quantity of backing welding, filling welding and cover surface welding to carry out single-side welding and double-side forming; performing hydrogen elimination treatment after welding; and (5) processing the weld reinforcement. The welding joint of the invention has good obdurability and cold bending performance: the tensile strength is more than or equal to 1000 MPa; d =6a, and 180 ° of face bending and back bending are both qualified; the impact energy of the welding seam, the fusion zone and the heat affected zone is more than or equal to 27J at minus 40 ℃; meanwhile, the welding process has strong operability, is convenient for industrial application, has high production efficiency and has popularization and application prospects.
Description
Technical Field
The invention belongs to the technical field of Gas Metal Arc Welding (GMAW), and particularly relates to a GMAW welding method for a low-alloy ultrahigh-strength steel Q1100E thin plate.
Background
In the face of the increasingly serious problems of environment, resources, energy, cost and the like, the green manufacturing road with large size, light weight and high efficiency becomes the development direction, and the market demand of the low-alloy ultrahigh-strength steel with the yield strength of 1100MPa or above is continuously expanded, such as a large-tonnage truck crane, a heavy-duty crawler crane, a large concrete pump truck and the like. However, with the increase of the strength of the steel plate, the welding difficulty is increased, and the phenomena of cold cracks, obvious decrease of strength, deterioration of impact toughness, cold bending cracking and the like often occur on a welding joint, so that the popularization and the use of the low-alloy ultrahigh-strength steel are seriously restricted.
Chinese patent CN102441727B discloses a gas shielded welding method for quenched and tempered low-alloy high-strength steel Q960E, and the thickness of a steel plate is 8-30 mm. After butt welding, the welding joint has good obdurability and cold bending performance: d =6a, the cold bending is qualified at 180 degrees and the impact toughness at-40 ℃ is more than or equal to 27J.
Chinese patent CN105522262B discloses a welding method of low-alloy ultrahigh-strength steel with yield strength of 1100MPa, which ensures that a welding joint does not generate cold cracks while ensuring the strength, but after 8 mm-thick steel plates are butt-welded, the 0 ℃ impact energy of a heat affected zone (0.5 mm away from a fusion line) is only 32J, and the cold bending performance of the steel plates is not detected.
Chinese patent CN105598596B discloses a non-preheating combined welding method for high-strength steel with tensile strength of 1200MPa, which uses welding wires of different types and grades during bottoming, filling, capping and back-sealing welding, and the tensile strength of a butt joint is only 780MPa although the tensile strength of a base metal is allowed to be more than or equal to 1200 MPa.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide a GMAW welding method for a low-alloy ultrahigh-strength steel Q1100E sheet, the thickness of a steel plate is 8-12 mm, V-shaped groove butt joint is adopted, single-side welding and double-side forming are carried out, and the tensile strength of a welding joint is ensured to be more than or equal to 1000MPa by strictly controlling the preheating temperature, the interlayer temperature, the heat input quantity, the post-welding dehydrogenation treatment and other processes; d =6a, and 180 ° of face bending and back bending are both qualified; the impact energy of the welding seam, the fusion zone and the heat affected zone is more than or equal to 27J at minus 40 ℃.
The technical scheme of the invention is as follows:
a GMAW welding method for a low-alloy ultrahigh-strength steel Q1100E thin plate comprises the following chemical components in percentage by weight: c = 0.15-0.20, Si = 0.10-0.30, Mn = 0.80-1.20, P ≤ 0.015, S ≤ 0.003, Al = 0.02-0.05, Nb = 0.01-0.02, V = 0.03-0.06, Ti = 0.008-0.020, Cr = 0.10-0.30, Mo = 0.50-0.80, Ni ≤ 0.50, B = 0.0015-0.004, and CEV = C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15= 0.52-0.56, the balance being Fe and unavoidable impurities; the thickness of the steel plate is 8-12 mm, the yield strength is more than or equal to 1100MPa, the tensile strength is more than or equal to 1300MPa, the elongation is more than or equal to 15%, and the impact energy at minus 40 ℃ is more than or equal to 27J; adopting 980MPa high-strength steel welding wires to carry out combined butt joint with the same plate thickness, and the method specifically comprises the following steps:
(1) groove machining: forming a V-shaped groove, wherein the angle of the groove is 60 +/-5 degrees, and the groove is not truncated;
(2) pretreatment: polishing and cleaning the groove by using a manual grinding wheel, removing iron scales and scrap iron, and cleaning iron rust and oil stains on the surfaces within 25mm of the two sides of the groove; controlling the assembly gap of the welding joint to be 2-3 mm, and fixing the two ends of the test plate by using an arc striking plate and an arc extinguishing plate;
(3) welding: GMAW welding is carried out by adopting a single-side welding and double-side forming method, the shielding gas is a mixed gas of argon and carbon dioxide, the gas flow is 18-22L/min, wherein the volume percentage of argon is 75-85%, and the volume percentage of carbon dioxide is 15-25%; preheating the test plate at 180-200 ℃ before welding; when welding, adopting direct current reverse connection, and sequentially carrying out backing welding with heat input of 12-13 kJ/cm, filling welding with 1-2 paths of heat input of 7-8 kJ/cm and cover surface welding with heat input of 10-12 kJ/cm; controlling the interlayer temperature to be 110-130 ℃ before filling welding and cover surface welding; controlling the weld reinforcement height to be 1-2 mm;
(4) and (3) post-welding hydrogen elimination treatment: after welding, carrying out heat preservation treatment on the test plate, and controlling the temperature of the test plate to be more than 100 ℃ and the cooling time to be more than or equal to 4 h;
(5) and (3) weld reinforcement treatment: and removing the weld reinforcement by adopting a mechanical method, polishing the weld to be flat and smooth by using a manual grinding wheel, and planing or polishing along the welding direction.
Further, the process parameters in the step (3) are optimized:
the parameters of the backing welding process are as follows: the welding voltage is 21-23V, the welding current is 180-210A, and the welding speed is 18-22 cm/min;
the parameters of the filling welding process are as follows: the welding voltage is 18-21V, the welding current is 150-180A, and the welding speed is 24-28 cm/min;
the parameters of the cover surface welding process are as follows: the welding voltage is 23-26V, the welding current is 210-240A, and the welding speed is 28-32 cm/min.
Preferably, the 980MPa high-strength steel welding wire has the diameter of 1.2mm, and the deposited metal mechanical properties are as follows: the tensile strength is more than or equal to 980MPa, the yield strength is more than or equal to 890MPa, the elongation is more than or equal to 15 percent, and the impact energy at minus 40 ℃ is more than or equal to 47J; the main chemical components and the weight percentage are as follows: c = 0.07-0.12, Si = 0.40-0.90, Mn = 1.20-2.00, Cr = 0.30-0.80, Mo = 0.30-0.80, Ni = 2.0-3.0, P is less than or equal to 0.015, S is less than or equal to 0.015, and the balance of Fe and inevitable impurities.
More preferably, the 980MPa high-strength steel welding wire comprises the following main chemical components in percentage by weight: c =0.10, Si =0.80, Mn =1.80, Cr =0.35, Mo =0.60, Ni =2.25, P =0.014, S =0.013, and the balance Fe and unavoidable impurities.
The technical principle of the invention is as follows: the low-alloy ultrahigh-strength steel has high carbon content and large carbon equivalent, the microstructure of a heat affected zone is transformed from granular bainite and a large number of M-A components to a mixed structure of lath bainite and lath martensite along with the increase of the cooling speed, and finally, all lath martensite structures are obtained. The mixed structure of lath bainite and lath martensite is mutually intersected, so that the effective grain size can be refined, and the number of large-angle grain boundaries can be increased, thereby effectively hindering the expansion of cracks and ensuring that the cracks have good toughness; the sufficient number of fine M-A components improve the plasticity due to the effect of the deformation induced martensite phase transformation, can effectively improve the cold bending performance, but form a massive M-A component with larger size when the cooling speed is very low, which is unfavorable for impact toughness, and the welding heat input quantity is often larger when the cooling speed is low, so that the original austenite grain size of a heat affected zone is coarsened, thereby obviously reducing the toughness and the plasticity of the heat affected zone, particularly the weld line. According to the practical result of the comparative example, when the welding heat input is small, the impact toughness of the welding joint reaches the standard, but the cold bending performance is unqualified; when the welding heat input is large, the cold bending performance of the welding joint is qualified, but the impact toughness does not meet the requirement. Therefore, the invention elaborately designs the cooling speed of each welding pass by controlling different heat input quantities of backing welding, filling welding and cover surface welding, preheating temperature, interlayer temperature, postweld heat treatment and other welding process parameters, obtains a structure with better central toughness and better surface plasticity in thickness, and solves the contradiction between the impact toughness and the cold bending performance of the low-alloy ultrahigh-strength steel welding joint.
The invention has the beneficial effects that: the welding method provided by the invention realizes GMAW welding of a low-alloy ultrahigh-strength steel Q1100E thin plate, a welding joint has good strength and toughness, cold bending property and cold crack resistance, meanwhile, the welding method has strong process operability, is convenient for industrial application, has high production efficiency, and can solve the welding problem when ultrahigh-strength steel is used at the key bearing part of large-scale equipment in the engineering machinery industry at present, thereby realizing light weight of equipment, reducing consumption of steel and energy, and reducing pollution to the environment. In addition, the welding method has reference significance for welding the low-alloy ultrahigh-strength steel with thicker Q1100E and higher strength, and is worthy of popularization and application.
Drawings
Fig. 1 is a schematic view of a butt weld joint, wherein 1 is a backing weld bead, 2 is a filling weld bead, and 3 is a facing weld bead.
FIGS. 2 to 4 are photographs showing metallographic structures of coarse grain heat affected zones of a backing weld bead, a filling weld bead and a facing weld bead of a welded joint in example 1.
Detailed Description
The invention performs GMAW welding on low-alloy ultrahigh-strength steel Q1100E thin plates, and the specific implementation mode is illustrated by examples 1-3, and comparison is performed by adopting comparative examples 1-1 and 1-2 and example 1 of the invention.
The welding apparatus of the example employed a Lincoln 455M/STT.
In the parent material tensile test of the embodiment, an extensometer is used for determining the yield strength by referring to the GB/T228 standard; the tensile test of the welded joint is referred to the GB/T2651 standard.
In the examples, the base material impact test was performed in accordance with GB/T229 standard, and the weld joint impact test was performed in accordance with GB/T2650 standard.
Examples cold bend testing of welded joints is referred to the GB/T2653 standard.
The welding test plates of the embodiment 1, the comparative example 1-1 and the comparative example 1-2 adopt the same base material, and the thickness of the steel plate is 8 mm; the steel comprises the following components in percentage by weight: c =0.16, Si =0.18, Mn =1.13, P =0.008, S =0.0013, Al =0.036, Nb =0.015, V =0.05, Ti =0.016, Cr =0.21, Mo =0.55, Ni =0.30, B =0.0019, CEV =0.53, and the balance being Fe and unavoidable impurities; the yield strength is 1176MPa, the tensile strength is 1346MPa, the elongation is 16 percent, and the impact energy at minus 40 ℃ is 70J/67J/69J (the sample size is 5mm multiplied by 10mm multiplied by 55 mm).
The welding test plate of example 2 was taken from a 10mm thick Q1100E steel plate, the steel having the following composition and weight percentages: c =0.18, Si =0.26, Mn =0.95, P =0.011, S =0.0025, Al =0.042, Nb =0.016, V =0.037, Ti =0.010, Cr =0.28, Mo =0.57, Ni =0.02, B =0.0018, CEV =0.52, the balance being Fe and unavoidable impurities; the yield strength was 1200MPa, the tensile strength was 1390MPa, the elongation was 17%, and the work of impact at-40 ℃ was 72J/60J/58J (specimen size was 7.5 mm. times.10 mm. times.55 mm).
The welding test plate of example 3 was taken from a 12mm thick Q1100E steel plate, the steel having the following composition and weight percentages: c =0.19, Si =0.25, Mn =0.85, P =0.009, S =0.002, Al =0.025, Nb =0.012, V =0.056, Ti =0.012, Cr =0.20, Mo =0.75, Ni =0.40, B =0.0022, CEV =0.56, and the balance is Fe and unavoidable impurities; the yield strength is 1149MPa, the tensile strength is 1374MPa, the elongation is 15.5 percent, and the impact energy at-40 ℃ is 72J/64J/69J (the sample size is 10mm multiplied by 55 mm).
The 980MPa high strength steel wire used in the examples was a type T Union GM-120 commercially available. The diameter of the welding wire is 1.2 mm; the deposited metal has the following mechanical properties: the tensile strength is more than or equal to 980MPa, the yield strength is more than or equal to 890MPa, the elongation is more than or equal to 15 percent, and the impact energy at minus 40 ℃ is more than or equal to 47J; the main chemical components and the weight percentage are as follows: c =0.10, Si =0.80, Mn =1.80, Cr =0.35, Mo =0.60, Ni =2.25, P =0.014, S =0.013, and the balance Fe and unavoidable impurities.
The embodiment adopts the combined butt welding with the same plate thickness, and comprises the following specific steps:
(1) groove machining: and a V-shaped groove is formed, the angle of the groove is 60 +/-5 degrees, and the groove is not truncated.
(2) Pretreatment: polishing and cleaning the groove by using a manual grinding wheel, removing iron scales and scrap iron, and cleaning iron rust and oil stains on the surfaces within 25mm of the two sides of the groove; and controlling the assembly gap of the welding joint assembly to be 2-3 mm, and fixing the two ends of the test plate by using an arc striking plate and an arc extinguishing plate.
(3) Welding: GMAW welding is carried out by adopting a single-side welding and double-side forming method, the shielding gas is a mixed gas of argon and carbon dioxide, the gas flow is 18-22L/min, wherein the volume percentage of argon is 75-85%, and the volume percentage of carbon dioxide is 15-25%; preheating the test plate at 180-200 ℃ before welding; when welding, adopting direct current reverse connection, and sequentially carrying out backing welding with heat input of 12-13 kJ/cm, filling welding with 1-2 paths of heat input of 7-8 kJ/cm and cover surface welding with heat input of 10-12 kJ/cm; strictly controlling the interlayer temperature between 110 and 130 ℃ before filling welding and cover surface welding; and controlling the weld reinforcement height to be 1-2 mm.
(4) And (3) post-welding hydrogen elimination treatment: after welding, the test plate is subjected to heat preservation treatment, and the cooling time of the test plate is controlled to be more than or equal to 4 hours at the temperature of more than 100 ℃.
(5) And (3) weld reinforcement treatment: and removing the weld reinforcement by adopting a mechanical method, polishing the weld to be flat and smooth by using a manual grinding wheel, and planing or polishing along the welding direction.
The key welding process parameters of the examples and comparative examples are shown in tables 1 to 5.
Table 1 key welding process parameters for example 1
TABLE 2 Key welding Process parameters for comparative examples 1-1
TABLE 3 Key welding Process parameters for comparative examples 1-2
Table 4 key welding process parameters for example 2
Table 5 key welding process parameters for example 3
The welding joint Q1100E welded by the process has good fusion condition, no macrocracks on the surface and the root, and qualified ultrasonic flaw detection inspection. The mechanical properties of the welded joints of example 1, comparative examples 1 to 2, example 2 and example 3 were examined as shown in Table 6. Therefore, in the examples 1, 2 and 3 which are carried out according to the welding method, the welded joint has good strength and toughness and cold bending performance and can meet the standard and use requirements, and the GMAW welding method provided by the invention is suitable for welding the low-alloy ultrahigh-strength steel Q1100E thin plate; the welding heat input amount of the comparative example 1-1 is large, the cold bending performance of the welding joint is qualified, but the impact toughness of the heat affected zone and the fusion line is lower than the standard value of 27J, the welding heat input amount of the comparative example 1-2 is small, the impact toughness of the welding joint is high, but the cold bending performance is unstable, particularly, the back bending is not qualified, and all parts are broken, so that the welding method provided by the invention further shows the superiority, the practicability and the reliability when the welding method is used for welding the low-alloy ultrahigh-strength steel Q1100E thin plate.
TABLE 6 mechanical properties of weld joints of examples and comparative examples
In addition, fig. 1 is a schematic diagram of a butt-welded joint of the invention, fig. 2 to 4 are metallographic structure photographs of coarse-grained heat-affected zones at different thicknesses of the welded joint of example 1, and it can be seen that according to the welding method of the invention, the structures of the heat-affected zones corresponding to different weld passes are different, the coarse-grained heat-affected zones of the backing weld and the cover weld have more M-a components, which are mixed structures of granular bainite, lath martensite and M-a components, and the coarse-grained heat-affected zones of the filling weld mainly have structures of lath martensite and lath bainite. This difference in structure across the thickness ensures that the welded joint has good impact toughness as well as good cold bend properties.
Claims (4)
1. The GMAW welding method of the low-alloy ultrahigh-strength steel Q1100E thin plate is characterized in that the components and the weight percentage of the steel are C = 0.15-0.20, Si = 0.10-0.30, Mn = 0.80-1.20, P is less than or equal to 0.015, S is less than or equal to 0.003, Al = 0.02-0.05, Nb = 0.01-0.02, V = 0.03-0.06, Ti = 0.008-0.020, Cr = 0.10-0.30, Mo = 0.50-0.80, Ni is less than or equal to 0.50, B = 0.0015-0.004, CEV = C + Mn/6+ (Cr + Mo + V)/5+ (Ni + Cu)/15= 0.52-0.56, and the balance is Fe and inevitable impurities; the thickness of the steel plate is 8-12 mm, the yield strength is more than or equal to 1100MPa, the tensile strength is more than or equal to 1300MPa, the elongation is more than or equal to 15%, and the impact energy at-40 ℃ is more than or equal to 27J; the welding wire is made of 980MPa high-strength steel, and comprises the following chemical components, by weight, C = 0.07-0.12, Si = 0.40-0.90, Mn = 1.20-2.00, Cr = 0.30-0.80, Mo = 0.30-0.80, Ni = 2.0-3.0, P is less than or equal to 0.015, S is less than or equal to 0.015, and the balance of Fe and inevitable impurities; the diameter of the welding wire is 1.2mm, and the mechanical properties of deposited metal are as follows: the tensile strength is more than or equal to 980MPa, the yield strength is more than or equal to 890MPa, the elongation is more than or equal to 15 percent, and the impact energy at the temperature of minus 40 ℃ is more than or equal to 47J; carrying out combined butt joint with the same plate thickness; the method comprises the following specific steps:
(1) groove machining: forming a V-shaped groove, wherein the angle of the groove is 60 +/-5 degrees, and the groove is not truncated;
(2) pretreatment: polishing and cleaning the groove by using a manual grinding wheel, removing iron scales and scrap iron, and cleaning iron rust and oil stains on the surfaces within 25mm of the two sides of the groove; controlling the assembly gap of the welding joint to be 2-3 mm, and fixing the two ends of the test plate by using an arc striking plate and an arc extinguishing plate;
(3) welding: GMAW welding is carried out by adopting a single-side welding and double-side forming method, the shielding gas is a mixed gas of argon and carbon dioxide, the gas flow is 18-22L/min, wherein the volume percentage of argon is 75-85%, and the volume percentage of carbon dioxide is 15-25%; preheating the test plate at 180-200 ℃ before welding; when welding, adopting direct current reverse connection, and sequentially carrying out backing welding with heat input of 12-13 kJ/cm, filling welding with 1-2 paths of heat input of 7-8 kJ/cm and cover surface welding with heat input of 10-12 kJ/cm; strictly controlling the interlayer temperature between 110 and 130 ℃ before filling welding and cover surface welding; controlling the weld reinforcement height to be 1-2 mm;
(4) and (3) post-welding hydrogen elimination treatment: after welding, carrying out heat preservation treatment on the test plate, and controlling the temperature of the test plate to be more than 100 ℃ and the cooling time to be more than or equal to 4 h;
(5) and (3) weld reinforcement treatment: and removing the weld reinforcement by adopting a mechanical method, polishing the weld to be flat and smooth by using a manual grinding wheel, and planing or polishing along the welding direction.
2. The GMAW welding method for the low-alloy ultrahigh-strength steel Q1100E thin plate according to claim 1, wherein the GMAW welding method comprises the following steps: the backing welding process parameters related in the step (3) are that the welding voltage is 21-23V, the welding current is 180-210A, and the welding speed is 18-22 cm/min.
3. The GMAW welding method for the low-alloy ultrahigh-strength steel Q1100E thin plate according to claim 1, wherein the GMAW welding method comprises the following steps: the filling welding process parameters related in the step (3) are as follows: the welding voltage is 18-21V, the welding current is 150-180A, and the welding speed is 24-28 cm/min.
4. The GMAW welding method for the low-alloy ultrahigh-strength steel Q1100E thin plate according to claim 1, wherein the GMAW welding method comprises the following steps: the parameters of the cover surface welding process related in the step (3) are that the welding voltage is 23-26V, the welding current is 210-240A, and the welding speed is 28-32 cm/min.
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| CN111872561B (en) * | 2020-06-10 | 2021-10-29 | 中国兵器科学研究院宁波分院 | Welding joint and welding method of low-alloy ultrahigh-strength steel |
| CN112453656A (en) * | 2020-10-09 | 2021-03-09 | 江阴兴澄特种钢铁有限公司 | Welding method of thin-wall thick high-strength steel plate |
| CN113118597A (en) * | 2021-03-30 | 2021-07-16 | 湖南华菱涟钢特种新材料有限公司 | Welding method of high-strength steel |
| CN114131159A (en) * | 2021-11-26 | 2022-03-04 | 湖南华菱湘潭钢铁有限公司 | Welding method of ultrahigh-strength steel Q1300E steel plate |
| CN114769804A (en) * | 2022-02-28 | 2022-07-22 | 南京钢铁股份有限公司 | Gas shielded welding method for 890-grade ultrahigh-strength marine board |
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