WO2023025242A1 - 钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件 - Google Patents

钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件 Download PDF

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WO2023025242A1
WO2023025242A1 PCT/CN2022/114784 CN2022114784W WO2023025242A1 WO 2023025242 A1 WO2023025242 A1 WO 2023025242A1 CN 2022114784 W CN2022114784 W CN 2022114784W WO 2023025242 A1 WO2023025242 A1 WO 2023025242A1
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Prior art keywords
welded
welding
hot stamping
steel plate
tailor
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PCT/CN2022/114784
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English (en)
French (fr)
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潘华
刘成杰
吴天海
雷鸣
孙中渠
蒋浩民
王舒扬
吴岳
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宝山钢铁股份有限公司
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Priority to KR1020247007824A priority Critical patent/KR20240050361A/ko
Priority to CA3229639A priority patent/CA3229639A1/en
Priority to AU2022334395A priority patent/AU2022334395A1/en
Priority to EP22860588.7A priority patent/EP4393631A1/en
Publication of WO2023025242A1 publication Critical patent/WO2023025242A1/zh

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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
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/346—Working by laser beam, e.g. welding, cutting or boring in combination with welding or cutting covered by groups B23K5/00 - B23K25/00, e.g. in combination with resistance welding
    • B23K26/348—Working by laser beam, e.g. welding, cutting or boring in combination with welding or cutting covered by groups B23K5/00 - B23K25/00, e.g. in combination with resistance welding in combination with arc heating, e.g. TIG [tungsten inert gas], MIG [metal inert gas] or plasma welding
    • 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
    • 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
    • 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
    • B23K26/32—Bonding taking account of the properties of the material involved
    • B23K26/323—Bonding taking account of the properties of the material involved involving parts made of dissimilar metallic material
    • 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
    • B23K26/60—Preliminary treatment
    • 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
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
    • 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

Definitions

  • the invention relates to a manufacturing method of a welded part, in particular to a manufacturing method of a steel thin-walled tailor welded part and a hot stamping part prepared by using the tailored welded part.
  • Tailored weldment is to weld together several steel plates of the same/different material, same/different thickness or same/different coating to meet the different requirements of parts for material properties.
  • the hot stamping process of tailor-welded parts can reduce the weight of the car body, improve the assembly accuracy and simplify the assembly steps. At the same time, it can take into account the advantages of hot stamping and further improve the formability of the steel plate.
  • the hot stamping products formed by tailor-welded parts have the characteristics of high strength, complex shape, good formability, high dimensional accuracy and small springback.
  • Steel for hot stamping can be divided into bare plate and coated steel plate according to the state of the surface.
  • the surface of bare steel is prone to oxidation at high temperature and forms scale.
  • the scale is squeezed Pressed into the steel, forming surface defects, which greatly affects its performance.
  • the hot stamping steel plate with coating can save the shot peening after hot stamping while protecting the steel plate from oxidation. Therefore, the coated steel plate Hot-stamped steel sheets have received more and more attention.
  • Chinese patent CN101426612A discloses "method for manufacturing welded parts with good mechanical properties from rolled coated sheet”. This method solves the problem that the strength and elongation of the weld seam are not up to standard due to the melting of aluminum into the molten pool, but the coating needs to be ablated before welding the steel plate, which increases equipment investment and reduces production efficiency.
  • Cikon patent CN102985216A discloses "arc/laser hybrid welding method for aluminum-coated steel parts with nitrogen and/or oxygen-containing gas".
  • arc+laser hybrid welding is used for welding aluminum-coated parts, and the shielding gas is added with additional gas nitrogen.
  • additional gas nitrogen the volume content of the additional gas is 1-20%
  • the function of the additional gas is to capture aluminum to form Al 2 O 3 or AlN compounds, to avoid the formation of ferrite or other harmful intermetallic compounds
  • the formed aluminum oxide or nitrogen Aluminum oxide floats on the surface of the molten pool, thus preventing aluminum from dissolving in the welded pool (paragraph 0015), and the weld structure is a full martensitic structure.
  • Chinese patent CN108025400A discloses "laser welding method for producing semi-finished plates from hardenable steel with aluminum-based or aluminum-silicon-based coating", which is tailored for differential strength hot stamping steel plates, and the final weld structure obtained is full horse Body organization.
  • Chinese patent CN201380027064.4 discloses "metal sheet with welding notches and its forming method".
  • it is difficult to control the depth of coating removal because if the coating removal is not complete, it will be similar to the method disclosed in Chinese patent CN101426612A; if the coating removal depth is too large, it will be Damage to the steel substrate is equivalent to the thinning of the material in disguise, and the performance of the joint after welding will inevitably decrease; in addition, the control of the removal width of the coating is also a problem.
  • the removal width is narrower than the weld seam, the coating elements will melt into the molten pool during welding, which will reduce the performance of the weld seam; if the removal width is wider than the weld seam, there will be no coating protection in the welding heat-affected zone, which will affect the corrosion resistance of the joint.
  • Cid patent CN104023899A discloses "tailored welded parts and its manufacturing method, and hot stamping parts using tailored welded parts", which uses welding wires with higher carbon and manganese content than the base metal to weld aluminum or aluminum alloy clad plates; although The problem of weld performance is solved, but the weld structure of the weld is completely transformed into martensite during hot stamping, and the carbon and manganese contents in the welding wire are 0.1-0.8wt.% and 1.5-7.0wt.% higher than the base metal respectively .
  • the content of carbon, manganese and other elements in hot stamping steel itself is very high, so the welding wire disclosed in the patent is a high-carbon and high-manganese welding wire, and the manufacturing difficulty of the welding wire is high.
  • Chinese patent CN111230301A discloses the "manufacturing method of steel thin-walled welding and other strong parts with aluminum or aluminum alloy coating".
  • the welded joints obtained by this method can only reach the level of 1500MPa.
  • the welded joints of hot stamping parts are subject to quasi-static stretching because the strength of the weld is lower than that of the base material, resulting in weld fracture , the depot cannot be used.
  • the purpose of the present invention is to provide a manufacturing method of steel thin-walled tailor-welded parts and hot stamping parts prepared by using the tailored welded parts, so as to solve the problem that the welded parts are welded after hot stamping due to the plating layer melting into the molten pool during the tailor-welded process.
  • the quasi-static tensile fracture position of the welded joint of the hot stamping part obtained by using the tailor-welded part is located in the base metal, the elongation of the joint is greater than 4%, and the weld strength is greater than the tensile strength of the low-strength base metal; welding
  • the strain rate of the joint is 40-800/s, its tensile fracture strain value is greater than 0.08, which better meets the application requirements in the field of automobile production.
  • a manufacturing method of steel thin-walled tailor-welded parts comprising the steps of:
  • the steel plates to be welded include a substrate and an aluminum or aluminum alloy coating on at least one surface thereof, and the coating includes a The contacted intermetallic compound alloy layer and the metal alloy layer thereon, the coating of the steel plate to be welded is not removed or thinned;
  • the welding speed in laser wire-filled welding is 40-120mm/s, and the wire-feeding speed is 2-8m/min;
  • the welding speed of MAG welding is 300-800mm/min
  • the welding speed of laser MAG hybrid welding is 40 ⁇ 150mm/s, and the wire feeding speed is 2 ⁇ 10m/min;
  • the protective gas is Ar+15 ⁇ 80vol.%CO 2 +1 ⁇ 10vol.%N 2 , and the flow rate of the protective gas is 10 ⁇ 25L/min;
  • the composition of the welding wire for welding includes C, Mn, and Ni austenite stabilizing elements, the content of the three elements in the welding wire composition is subtracted from the content of the corresponding element in the steel plate A to be welded, and the obtained difference is expressed by ⁇ C, ⁇ Mn and ⁇ Ni represent;
  • the steel plate to be welded A is one of the two steel plates to be welded with the same strength level, or the steel plate to be welded with a lower strength level among the two steel plates to be welded with different strength levels;
  • the tensile strength of steel plate A to be welded is ⁇ 900MPa, ⁇ C: -0.05 ⁇ 0.09wt.%, ⁇ Mn: -0.5wt.% ⁇ 1.4wt.%, ⁇ Ni: 0 ⁇ 4.0wt.%; or
  • the tensile strength of steel plate A to be welded is ⁇ 1700MPa, ⁇ C: -0.26 ⁇ -0.15wt.%, ⁇ Mn: -1.4 ⁇ 0.7wt.%, ⁇ Ni: 2.26 ⁇ 4.0wt%;
  • the weld structure of the tailored weldment is martensite + 1-15vol.% ferrite dispersedly distributed + 0-5vol.% retained austenite; the content of free aluminum in the weld is 0.1-4.0wt.%. .
  • the CO 2 content in the protective gas is 15-50 vol.%.
  • the N 2 content in the protective gas is 2-4 vol.%.
  • the welding current of the MAG welding or laser MAG hybrid welding is 110-130A, and the welding voltage is 18-25V.
  • the welding current of the MAG welding or laser MAG hybrid welding is 110-125A, and the welding voltage is 18-25V.
  • the welding speed of laser MAG hybrid welding is 60-150 mm/s, and the wire feeding speed is 4-10 m/min.
  • the defocus amount in the laser wire-fill welding or laser MAG composite welding process is -10-10mm, and the laser power control range is 3-8kW.
  • the defocus amount is -8-8mm, and the laser power control range is 4-8kW.
  • the minimum diameter of the laser spot output by the laser processing head is 0.3-1.6 mm.
  • those skilled in the art can select relevant parameters according to the actual situation, so as to ensure that the minimum spot diameter output by the laser processing head is 0.3-1.6 mm.
  • the ratio of the focal length of the focusing mirror to the focal length of the collimating mirror can be set to 0.75 ⁇ 4.0
  • the Rayleigh Length is 1.249 ⁇ 44.955
  • the diameter of the laser transmission fiber is 0.2 ⁇ 0.8mm
  • the Focusing Angle is 2.3 ⁇ 18.4 Grad.
  • the welding is laser wire-filled welding
  • the welding speed is 40-120mm/s
  • the wire-feeding speed is 2-8m/min
  • the defocus is -8-8mm
  • the laser power control range is 4 ⁇ 8kW.
  • the welding is MAG welding
  • the welding speed is 400-800mm/min
  • the welding current is 110-125A
  • the welding voltage is 18-25V.
  • the welding is laser MAG hybrid welding
  • the welding speed is 60-150mm/s
  • the wire feeding speed is 4-10m/min
  • the defocus is -10-10mm
  • the laser power control range is 3 ⁇ 8kW
  • welding current is 110 ⁇ 130A
  • welding voltage is 18 ⁇ 25V.
  • the diameter of the welding wire is 1.0-1.6 mm.
  • the thickness of the substrate is 0.5-3mm.
  • the coating is an aluminum alloy coating
  • the composition of the aluminum alloy coating is: Si: 5-11%, Fe: 0-4%, and the balance is Al and other unavoidable impurities.
  • the composition of the aluminum alloy coating is: Si: 8.5-10.5%, Fe: 1.5-2.5%, and the balance is Al and other unavoidable impurities.
  • the tensile strength of the steel plate A to be welded is ⁇ 900MPa, and its component weight percentage is: C: 0.06-0.1%, 0 ⁇ Si ⁇ 0.1%, Mn: 0.5-1.0%, P ⁇ 0.03%, S ⁇ 0.01%, Al ⁇ 0.1%, 0 ⁇ Cr ⁇ 0.1%, 0 ⁇ Ti ⁇ 0.05%, and the rest are Fe and other unavoidable impurities.
  • the tensile strength of the steel plate A to be welded is greater than or equal to 900MPa and less than 1300MPa, and its composition weight percentage is: C: 0.06-0.15%, Si: 0.3-1.0%, Mn: 0.5-2.5%, P ⁇ 0.10% , S ⁇ 0.05%, Al: 0.02 ⁇ 0.30%, Cr: 0.05 ⁇ 0.5%, Nb: 0.02 ⁇ 0.20%, V ⁇ 0.15%, Ti: 0.01 ⁇ 0.10%, Mo ⁇ 0.5%, Ni ⁇ 0.5%, B : 0.001 to 0.01%, the balance being Fe and other unavoidable impurities.
  • the tensile strength of the steel plate A to be welded is greater than or equal to 1300MPa and less than 1700MPa, and its composition weight percentage is: C: 0.2-0.3%, Si: 0.1-0.5%, Mn: 0.5-2.5%, P ⁇ 0.015% , S ⁇ 0.05%, Al ⁇ 0.1%, Ti ⁇ 0.2%, B: 0.0005 ⁇ 0.08%, Cr: 0.01 ⁇ 1%, Ni ⁇ 0.24%, and the balance is Fe and other unavoidable impurities.
  • the tensile strength of the steel plate A to be welded is ⁇ 1700 MPa, and its composition by weight percentage is: C: 0.30-0.39%, Si: 0.05-0.6%, Mn: 0.5-2.5%, P ⁇ 0.015%, S ⁇ 0.01%, Al: 0.01 ⁇ 0.07%, Cr ⁇ 1.0%, Nb ⁇ 0.08%, V ⁇ 0.1%, Ti: 0.01 ⁇ 0.12%, Mo: 0.01 ⁇ 0.5%, Ni ⁇ 0.25%, B: 0.0001 ⁇ 0.005 %, N ⁇ 0.006%, and the balance is Fe and other unavoidable impurities.
  • the composition of the welding wire is: C: 0.05-0.15%, Mn: 0.5-1.9%, Ni: 0-4%, and the balance is Fe and other unavoidable impurities.
  • the content of Ni in the welding wire is 0.5-4%. It should be understood that the selection of C, Mn and Ni content in the welding wire needs to meet the requirements mentioned above.
  • the invention includes the steel thin-walled tailor-welded parts obtained by the above-mentioned manufacturing method.
  • the present invention provides a steel thin-walled tailor welded part, which is welded by two steel plates to be welded with the same or different strength levels, the steel plates to be welded include a base body and aluminum on at least one surface thereof Or an aluminum alloy coating, the coating includes an intermetallic compound alloy layer in contact with the substrate and a metal alloy layer thereon, and the weld structure of the steel thin-walled tailor-welded part is martensite +1-15vol. % diffusely distributed ferrite + 0-5vol.% retained austenite, and the content of free aluminum in the weld is 0.1-4.0wt.%.
  • the thickness of the substrate is 0.5-3mm.
  • the coating is an aluminum alloy coating
  • the composition of the aluminum alloy coating is: Si: 5-11%, Fe: 0-4%, and the balance is Al and other unavoidable impurities.
  • the composition of the aluminum alloy coating is: Si: 8.5-10.5%, Fe: 1.5-2.5%, and the balance is Al and other unavoidable impurities.
  • the two steel plates to be welded are each independently selected from the following steel plates:
  • the composition weight percentage is: C: 0.06 ⁇ 0.1%, 0 ⁇ Si ⁇ 0.1%, Mn: 0.5 ⁇ 1.0%, P ⁇ 0.03%, S ⁇ 0.01%, Al ⁇ 0.1%, 0 ⁇ Cr ⁇ 0.1%, 0 ⁇ Ti ⁇ 0.05%, the rest are Fe and other unavoidable impurities;
  • the composition weight percentage is: C: 0.06-0.15%, Si: 0.3-1.0%, Mn: 0.5-2.5%, P ⁇ 0.10%, S ⁇ 0.05%, Al: 0.02 ⁇ 0.30%, Cr: 0.05 ⁇ 0.5%, Nb: 0.02 ⁇ 0.20%, V ⁇ 0.15%, Ti: 0.01 ⁇ 0.10%, Mo ⁇ 0.5%, Ni ⁇ 0.5%, B: 0.001 ⁇ 0.01%, balance For Fe and other unavoidable impurities;
  • the composition weight percentage is: C: 0.2-0.3%, Si: 0.1-0.5%, Mn: 0.5-2.5%, P ⁇ 0.015%, S ⁇ 0.05%, Al ⁇ 0.1%, Ti ⁇ 0.2%, B: 0.0005 ⁇ 0.08%, Cr: 0.01 ⁇ 1%, Ni ⁇ 0.24%, the balance is Fe and other unavoidable impurities; and
  • Steel plate with tensile strength ⁇ 1700MPa its composition by weight percentage is: C: 0.30 ⁇ 0.39%, Si: 0.05 ⁇ 0.6%, Mn: 0.5 ⁇ 2.5%, P ⁇ 0.015%, S ⁇ 0.01%, Al: 0.01 ⁇ 0.07%, Cr ⁇ 1.0%, Nb ⁇ 0.08%, V ⁇ 0.1%, Ti: 0.01 ⁇ 0.12%, Mo: 0.01 ⁇ 0.5%, Ni ⁇ 0.25%, B: 0.0001 ⁇ 0.005%, N ⁇ 0.006%, remainder The amount is Fe and other unavoidable impurities.
  • the present invention also provides a hot stamping part prepared from the steel thin-walled tailor-welded parts obtained by the above manufacturing method, the weld seam structure of the hot stamping part is martensite + 0.1-10vol.% ferrite dispersedly distributed , the quasi-static tensile fracture position of the hot stamping part is the base material, and the elongation of the joint is not less than 4%; when the strain rate of the welded joint is 40-800/s, the tensile fracture strain value of the welded joint is greater than 0.08.
  • the ferrite content in the weld structure of the hot stamping part of the present invention is 0.5-5 vol.%.
  • the ferrite in the weld microstructure of the hot stamping part of the present invention is needle-shaped.
  • the strain rate of the welded joint of the hot stamping part of the present invention is 40-800/s
  • the tensile fracture strain value of the welded joint is greater than 0.09.
  • iron-aluminum intermetallic compound and massive ferrite there is no iron-aluminum intermetallic compound and massive ferrite in the weld structure of the hot stamping part of the present invention.
  • the present invention also provides a hot stamping part, the welding seam structure of the hot stamping part is martensite + 0.1-10vol.% ferrite dispersedly distributed, the quasi-static tensile fracture position of the hot stamping part is the base material, and the joint is extended The rate is not less than 4%; when the strain rate of the welded joint is 40-800/s, the tensile fracture strain value of the welded joint is greater than 0.08.
  • the hot stamping parts are prepared by using the thin-walled steel tailor-welded parts of the present invention, or by using the thin-walled steel tailor-welded parts obtained by the manufacturing method described in the present invention.
  • the ferrite content in the weld structure of the hot stamping part of the present invention is 0.5-5 vol.%.
  • the ferrite in the weld microstructure of the hot stamping part of the present invention is needle-shaped.
  • the strain rate of the welded joint of the hot stamping part of the present invention is 40-800/s
  • the tensile fracture strain value of the welded joint is greater than 0.09.
  • iron-aluminum intermetallic compound and massive ferrite there is no iron-aluminum intermetallic compound and massive ferrite in the weld structure of the hot stamping part of the present invention.
  • the present invention also provides a method for preparing a hot stamping part, which includes the step of performing hot stamping and quenching on the steel thin-walled tailor welded part of the present invention.
  • the tailor welded blank is subjected to hot stamping and quenching, the heating temperature is 920-950° C., the heating time is 3-6 minutes, and the pressure is maintained in the water-passing mold for 8-20 seconds.
  • the method includes the step of manufacturing thin-walled tailor-welded steel parts by using the method for manufacturing thin-walled tailored welded parts made of steel according to any embodiment herein, and the manufactured thin-walled tailored welded steel parts The step of performing hot stamping and quenching.
  • the weld seam structure of the hot stamping part is martensite + 0.1-10vol.% ferrite dispersedly distributed
  • the quasi-static tensile fracture position of the welded joint of the hot stamping part is the base material
  • the elongation of the joint is not low
  • the strain rate of the welded joint is 40-800/s
  • the tensile fracture strain value of the welded joint is greater than 0.08.
  • the ferrite content in the weld structure of the hot stamping part is 0.5-5 vol.%.
  • the ferrite in the weld structure of the hot stamping part is needle-shaped.
  • the strain rate of the welded joint of the hot stamping part is 40-800/s
  • the tensile fracture strain value of the welded joint is greater than 0.09.
  • At least one surface of the substrate to be welded in the present invention has a coating on at least one surface.
  • the coating on the area to be welded on the steel plate to be welded is not removed or thinned. Due to the existence of the aluminum-containing coating, the coating melts The molten pool forms brittle and hard intermetallic compounds (Fe 3 Al, Fe 2 Al 5 , FeAl 3 ) and excessive ferrite, which reduces the strength and ductility of welded joints after hot stamping and cannot be used.
  • the amount of free aluminum in the weld should be controlled during the welding process to avoid the formation of iron-aluminum intermetallic compounds in the weld and the formation of an appropriate amount of ferrite.
  • the ternary shielding gas mixed with argon, carbon dioxide and nitrogen is used in the welding process.
  • the volume content of N2 is 1-10%.
  • N2 can transfer nitrogen element to the weld.
  • Al and N in the molten pool react, The formed AlN is dispersed in the molten pool with the violent stirring of the molten pool, and will be used as secondary phase particles to improve the strength of the weld after hot stamping; on the other hand, the free Al in the molten pool combines with N to form AlN, which controls the melting
  • the concentration of free Al in the pool can prevent the precipitation of excessive ferrite, and also avoid the absence of ferrite in the weld at room temperature.
  • the proportion of N2 in the shielding gas should not be too high, otherwise the ductility of the welded joint will be reduced, and nitrogen pores will also be caused.
  • the volume content of CO2 is 15-80%.
  • CO2 enhances the activity of the protective gas in the welding zone, which is beneficial to increase the penetration rate of the plate and the fluidity of the liquid metal, improve the composition uniformity of the molten pool metal, and avoid aluminum elements segregation, to ensure that the composition of the weld is uniform, to avoid the strip structure due to uneven composition, especially to avoid the large ferrite formed by the aggregation of aluminum, to ensure that the ferrite is dispersed in the weld, so that the weld The performance is stable.
  • the welding wire used in the welding process contains carbon, manganese, nickel and other elements that expand the austenite phase zone. Control the difference between the element content of carbon, manganese and nickel in the weld and the steel plate to be welded.
  • these three elements are elements that expand the austenite phase region, compressing the high-temperature ferrite region to prevent Excess ferrite is precipitated in the weld seam before the hot stamping die is closed to increase the strength of the weld seam; on the other hand, the martensite transformation temperature of the weld seam can be reduced to ensure the martensite transformation rate.
  • Carbon is an important constituent element of welding wire, which affects the machinability of welding wire and the carbon equivalent of weld.
  • the austenite stability of the weld decreases, and it is difficult to ensure the strength of the weld; when the carbon content is too high, the manufacturability of the welding wire decreases, and the plasticity and toughness of the weld decrease.
  • the content of C in the welding wire may be 0.05-0.15%.
  • manganese can improve the austenite stability of the weld, shift the C curve to the right, and reduce the critical cooling rate of martensite. If the manganese content is too high, the manufacturability of the welding wire will be affected, and the plasticity and toughness of the weld will decrease. If the Mn content is too low, the hardenability of the weld is reduced and the strengthening effect is weakened.
  • the content of Mn in the welding wire can be 0.5-1.9%.
  • nickel can increase the stability of austenite in the weld, reduce the critical Ms point temperature, and improve the hardenability, strength and toughness of the weld. If the nickel content is too high, the production cost of the welding wire will increase, and the residual austenite after hot stamping of the weld seam will increase, which will affect the strength of the weld seam; the nickel content of the welding wire can be adjusted according to the strength level of the plate to be welded to ensure that the weld seam toughness needs.
  • the content of Ni in the welding wire may be 0-4%, such as 0.5-4%.
  • the composition of the welding wire for welding is changed based on the composition of the steel plate to be welded at the low-strength steel level.
  • the composition of the welding wire can be changed accordingly, and the composition of the corresponding weld must also change.
  • the structure of the weld seam is the same, but the mechanical properties of the weld seam are different, so as to meet the performance requirements of the automobile industry for tailor-welded blanks with different strengths.
  • the present invention further controls welding speed and wire feeding speed, and changes the ratio of deposited metal (weld metal formed after welding wire is melted) in the weld, although the steel plate to be welded contains aluminum or aluminum Alloy coating, but the concentration of aluminum element melted into the weld of tailor welded parts can be controlled.
  • the concentration of free aluminum in the weld seam of the tailored weldment is controlled at 0.1-4.0wt.% through the joint action of the shielding gas, the composition of the welding wire and the welding process.
  • Al is an element that promotes the formation of ferrite. If the free Al in the weld is reduced, the ability of ferrite formation will be weakened.
  • the content of free Al in the weld should be controlled at 0.1-4.0wt.%. On the one hand, it can avoid It prevents excessive ferrite from being formed in the weld and ensures the strength of the weld; on the other hand, it can avoid the formation of iron-aluminum intermetallic compounds in the weld, and keep an appropriate amount of ferrite in the weld to ensure that tailor welding at room temperature
  • the weld structure of the workpiece is martensite + 1-15vol.% ferrite dispersedly distributed + 0-5vol.% retained austenite.
  • the focus is on regulating the weld structure of the tailor-welded parts, mainly regulating the quantity and shape of ferrite, avoiding the formation of iron-aluminum intermetallic compounds and massive ferrite during the welding process, and finally obtaining
  • the weld structure of tailor-welded parts is martensite + 1-15vol.% dispersed ferrite + 0-5vol.% residual austenite.
  • a proper amount of diffusely distributed ferrite in the weld of the part is kept below, and the weld structure of the finally obtained hot stamping part is martensite + 0.1-10vol.% ferrite dispersedly distributed.
  • the welding seam structure of the hot stamping part of the present invention is martensite + 0.1-10vol.% ferrite dispersedly distributed, which improves the high-speed tensile performance of the welded joint, and when the strain rate is 40-800/s, the fracture strain value of the welded joint Greater than 0.08.
  • the weld seam structure of traditional hot stamping parts is single martensite. When the strain rate is 40/s, the fracture strain value of the welded joint is about 0.07; when the strain rate is 800/s, the fracture strain value of the welded joint is about 0.058. Therefore, It can be seen that the high-speed tensile fracture strain value of the hot stamping part of the present invention is significantly improved.
  • the welded joint with martensite + dispersed acicular ferrite can provide more coordinated deformation opportunities for martensite when subjected to external force compared with the welded joint with single martensite.
  • the substructure of martensite is mainly dislocation, and the existence of ferrite will greatly reduce the dislocation density of martensite in the weld structure compared with that of single martensite; dislocation accumulation is easy Microcracks are formed, so the risk of forming microcracks in welded joints with martensite + diffusely distributed acicular ferrite is greatly reduced compared with welded joints with single martensite; even if microcracks are formed Cracks, dispersed ferrite can also hinder the further growth and expansion of micro-cracks, so that the welded joint structure is martensite + diffusely distributed acicular ferrite than the weld structure is a single martensite. Welded joints of astenite exhibit better deformability, especially during high-speed tensioning.
  • the invention adopts hot stamping steel plate with aluminum or aluminum alloy coating for tailor welding, controls the welding speed and wire feeding speed by adjusting the welding wire composition, and uses ternary shielding gas as the shielding gas to reduce the amount of free aluminum in the weld seam of tailor welded parts , the content of free aluminum in the weld is controlled at 0.1-4.0wt.%.
  • it avoids excessive ferrite in the weld and ensures the strength and toughness of the weld; on the other hand, it can avoid the formation of iron-aluminum metal in the weld inter-compound, and keep a proper amount of ferrite in the weld.
  • CO 2 in the shielding gas can avoid the segregation of aluminum elements, ensure the uniform composition of the weld, and avoid the formation of large ferrite due to aluminum aggregation.
  • the performance is more stable.
  • the obtained tailor-welded parts are hot stamped parts prepared by hot stamping. Due to the presence of AlN in the weld, the weld strength is further improved, and the quasi-static tensile fracture position of the welded joint is the base material, indicating that the weld strength is greater than that of the base metal. Meet the requirements of the automotive production field.
  • the present invention ensures that the weld structure of the tailored weldment is martensite + 1-15 vol. % dispersedly distributed ferrite + 0-5 vol. %retained austenite; in this way, martensite + 0.1-10vol.% dispersed ferrite is formed in the weld structure of the hot stamping parts obtained after hot stamping of tailor welded parts, and the weld structure is full martensite Compared with the hot stamping parts of the body, the high-speed tensile performance of the welded joints of the hot stamping parts of the present invention is significantly improved, and when the strain rate is 40-800/s, the fracture strain value of the welded joints is greater than 0.08.
  • thermoformed parts prepared by the tailor-welded parts obtained by the technical solution of the present invention have better high-speed deformation ability under the premise of ensuring quasi-static mechanical properties, absorb more energy during collisions, and have higher collision safety.
  • Fig. 1 is a schematic diagram of tailor welding with laser filler wire in Embodiment 1 of the present invention.
  • Fig. 2 is a curve diagram of quasi-static tensile properties of welded joints of hot stamping parts obtained in Example 1 of the present invention.
  • Fig. 3 is a diagram of quasi-static tensile sample fracture positions of welded joints of hot stamping parts obtained in Example 1 of the present invention.
  • Fig. 4 is a metallographic diagram of a welded joint of a hot stamping part obtained in Example 1 of the present invention.
  • Fig. 5 is the hardness distribution of the welded joint of the hot stamping part obtained in Example 1 of the present invention.
  • the laser filler wire tailor welding of the present invention uses the laser beam 40 to melt the welding wire 30 and the steel plate to be welded 10 and the steel plate to be welded 20 to realize tailor welding;
  • the steel plate to be welded 10 includes a steel matrix 11 and the coatings 12 and 12' on the base.
  • the steel plate 20 to be welded includes a steel base 21 and coatings 22 and 22' on the base.
  • the coatings are aluminum or aluminum alloy coatings.
  • Table 1 shows the composition of the steel plate 10 to be welded
  • Table 2 shows the composition of the steel plate 20 to be welded
  • Table 3 shows the composition of the welding wire of the present invention
  • Table 4 shows the quasi-static tension of the welded joint of the hot stamping part Performance
  • Table 5 shows the high-speed tensile properties of welded joints of hot stamping parts.
  • the manufacturing method of steel thin-walled tailor-welded parts according to the present invention comprises the following steps:
  • the two steel plates to be welded are welded by laser wire filler welding, MAG welding or laser MAG composite welding.
  • Examples 1-21 and comparative examples 1-2 relate to the weight percentages of Si and Fe components in the aluminum alloy coating of the steel plate to be welded, as shown in Table 1 and Table 2, and the balance is Al and other unavoidable impurities;
  • the strength levels 500MPa, 1000MPa, 1500MPa and 1800MPa involved in Examples 1-21 and Comparative Examples 1-2 refer to the tensile strength levels of the steel plates to be welded after hot stamping.
  • the tensile strength (tested according to ISO 6892 standard) ranges corresponding to these four strength levels are: 500MPa grade is 400-750MPa, 1000MPa grade is 1000-1300MPa, 1500MPa grade is 1300-1700MPa, 1800MPa grade is 1700-2150MPa.
  • the wire feeding speed is 4m/min
  • the wire diameter is 1.2mm
  • the shielding gas is 48vol.%Ar+50vol.% CO2 +2vol.% N2
  • the gas flow rate is 15L/min.
  • the heating temperature is 945°C
  • the heating time is 4 minutes
  • the pressure is maintained in the water-passing mold for 10 seconds.
  • the tailor-welded blank is first austenitized, and the atoms in the coating and the steel expand each other during this heating period, so that the original coating is completely transformed into an intermetallic compound layer, and the thickness of this layer is thicker than that of the original coating. .
  • this layer has the characteristics of high melting point and high hardness, which prevents the substrate from being oxidized and decarburized during the heating stage and holding pressure stage.
  • the tailor welded blank undergoes martensitic transformation.
  • the metallographic photo of the joint is shown in Figure 4.
  • the weld structure is martensite + 4.9vol.% diffusely distributed acicular ferrite, and no iron-aluminum intermetallic compound and massive ferrite are seen.
  • the hardness of the joint is shown in Figure 5. From Figure 5, it can be seen that the hardness consistency between the weld of the hot stamping part and the base metal is good.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the wire feeding speed is 2m/min
  • the wire diameter is 1.0mm
  • the shielding gas is 81vol.%Ar+15vol.% CO2 +4vol.% N2
  • the gas flow rate is 10L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filled tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.5mm is reserved for the spliced plate gap, the welding power is 7kW, the welding speed is 50mm/s, and the defocus amount is -10mm , the wire feeding speed is 8m/min, the wire diameter is 1.2mm, the shielding gas is 10vol.%Ar+80vol.%CO 2 +10vol.%N 2 , and the gas flow rate is 25L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Use the following process to carry out laser wire-filling tailor welding, using the welding wire of the present invention see Table 3 for the welding wire composition), reserve 0.1mm for the spliced plate gap, welding power 5kW, welding speed 120mm/s, defocus amount -5mm , the wire feeding speed is 7m/min, the wire diameter is 1.0mm, the shielding gas is 40vol.%Ar+50vol.%CO 2 +10vol.%N 2 , and the gas flow rate is 22L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filling tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.3mm is reserved for the gap between the spliced plates, the welding power is 8kW, the welding speed is 100mm/s, and the defocus amount is -8mm , the wire feeding speed is 6m/min, the wire diameter is 1.2mm, the shielding gas is 46vol.%Ar+50vol.%CO 2 +4vol.%N 2 , and the gas flow rate is 19L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Use the following process to carry out laser wire-filling tailor welding, using the welding wire described in the present invention see Table 3 for the welding wire composition), reserve 0.3mm for the splicing plate gap, welding power 5kW, welding speed 90mm/s, defocus amount -6mm , the wire feeding speed is 5m/min, the wire diameter is 1.2mm, the shielding gas is 83vol.%Ar+15vol.%CO 2 +2vol.%N 2 , and the gas flow rate is 21L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filling tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.4mm is reserved for the gap between the spliced plates, the welding power is 8kW, the welding speed is 100mm/s, and the defocus is 3mm.
  • the wire feeding speed is 3m/min
  • the wire diameter is 1.6mm
  • the shielding gas is 81vol.%Ar+18vol.% CO2 +1vol.% N2
  • the gas flow rate is 23L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Table 3 for the welding wire composition
  • the welding power is 8kW
  • the welding speed is 88mm/s
  • the defocus amount is -3mm
  • the wire feeding speed is 5m/min
  • the wire diameter is 1.2mm
  • the shielding gas is 74vol.%Ar+16vol.%CO 2 +10vol.%N 2
  • the gas flow rate is 18L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Use the following process to carry out laser wire-filling tailor welding adopt the welding wire of the present invention (see Table 3 for the welding wire composition), reserve 0.4mm for the gap between spliced plates, weld power 5.5kW, welding speed 80mm/s, defocus amount- 6mm, the wire feeding speed is 5.5m/min, the wire diameter is 1.2mm, the shielding gas is 58vol.%Ar+40vol.%CO 2 +2vol.%N 2 , and the gas flow rate is 17L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Use the following process to carry out laser wire-filling tailor welding adopt the welding wire of the present invention (see Table 3 for the welding wire composition), reserve 0.35mm for the spliced plate gap, weld power 7.5kW, welding speed 110mm/s, defocus amount- 7.5mm, wire feeding speed 7.5m/min, wire diameter 1.4mm, shielding gas 51vol.%Ar+45vol.%CO 2 +4vol.%N 2 , gas flow 19L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filling tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.25mm is reserved for the spliced plate gap, the welding power is 6.5kW, the welding speed is 85mm/s, and the defocus amount is - 5.5mm, wire feeding speed 5.5m/min, wire diameter 1.2mm, shielding gas 65vol.%Ar+30vol.%CO 2 +5vol.%N 2 , gas flow 12L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Adopt the following process to carry out laser wire filling tailor welding adopt the welding wire of the present invention (the welding wire composition is shown in Table 3), reserve 0.3mm for the spliced plate gap, welding power 7.5kW, welding speed 105mm/s, defocus amount- 4.5mm, wire feeding speed 8m/min, wire diameter 1.0mm, shielding gas 59vol.%Ar+35vol.%CO 2 +6vol.%N 2 , gas flow 14L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used to carry out laser filler wire tailor welding, using the welding wire of the present invention (the welding wire composition is shown in Table 3), the spliced plate gap is reserved for 0.35mm, the welding power is 4.5kW, the welding speed is 65mm/s, and the defocus amount is - 7mm, wire feeding speed 4.5m/min, wire diameter 1.2mm, shielding gas 67vol.%Ar+25vol.%CO 2 +8vol.%N 2 , gas flow rate 11L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used to carry out laser filler wire tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.2mm is reserved for the spliced plate gap, the welding power is 5.5kW, the welding speed is 70mm/s, and the defocus amount is - 6.5mm, wire feeding speed 5m/min, wire diameter 1.2mm, shielding gas 73vol.%Ar+20vol.%CO 2 +7vol.%N 2 , gas flow 16L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Adopt the following process to carry out arc tailor welding with active gas shielding of molten electrode adopt the welding wire according to the present invention (see Table 3 for the welding wire composition), reserve 0.4mm in the splicing plate gap; the welding current is 110A, the welding voltage is 22V, and the welding speed 500mm/min, the wire diameter is 1.2mm, the shielding gas is 76vol.%Ar+20vol.%CO 2 +4vol.%N 2 , and the gas flow rate is 13L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filling tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.3mm is reserved for the spliced plate gap, the welding power is 4kW, the welding speed is 60mm/s, and the defocus amount is -6.5 mm, the wire feeding speed is 4m/min, the wire diameter is 1.2mm, the shielding gas is 56vol.%Ar+35vol.%CO 2 +9vol.%N 2 , and the gas flow rate is 20L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used to carry out laser MAG composite tailor welding, using the welding wire according to the present invention (see Table 3 for the welding wire composition), welding power 3kW, welding speed 80mm/s, 0.3mm gap reserved for spliced plates, and defocus amount 2mm;
  • the current of the MAG heat source is 120A, the voltage is 20V;
  • the wire feeding speed is 6m/min, the wire diameter is 1.2mm;
  • the shielding gas is 78vol.%Ar+20vol.%CO 2 +2vol.%N 2 , and the gas flow rate is 24L/min .
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the following process is used for laser wire-filling tailor welding, using the welding wire of the present invention (see Table 3 for the welding wire composition), 0.1mm is reserved for the spliced plate gap, the welding power is 5kW, the welding speed is 85mm/s, and the defocus amount is -8.5 mm, the wire feeding speed is 6m/min, the wire diameter is 1.0mm, the shielding gas is 40vol.%Ar+50vol.%CO 2 +10vol.%N 2 , and the gas flow rate is 25L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • Table 3 for the welding wire composition
  • welding power is 5kW
  • welding speed is 83mm/s
  • defocus is -6mm
  • the wire feeding speed is 7m/min
  • the wire diameter is 1.2mm
  • the shielding gas is 40vol.%Ar+50vol.%CO 2 +10vol.%N 2
  • the gas flow rate is 19L/min.
  • Example 2 After welding, the same hot stamping process as in Example 1 is used for hot stamping.
  • the quasi-static tensile properties of welded joints of hot stamping parts are shown in Table 4.
  • the high-speed tensile properties of welded joints of hot stamping parts are shown in Table 5.
  • the weld microstructure of hot stamping parts obtained by ablation welding is full martensite.
  • the high-speed tensile test results of the prepared tailor-welded hot stamping parts are shown in Table 5, and the test was carried out with reference to the standard ISO/DIS 26203-2.
  • Table 5 The results of the high-speed tensile test of the welded joint are shown in Table 5, and the test was carried out with reference to the standard ISO/DIS 26203-2.
  • the quasi-static tensile fracture position of the welded joint of the hot stamping part obtained by the present invention is the base material, indicating that the strength of the weld seam is greater than that of the low-strength base material, which meets the requirements in the field of automobile production.
  • the high-speed tensile properties of the welded joints are significantly improved, and the fracture strain value of the welded joints is greater than 0.09 when the strain rate is 40-800/s.
  • thermoformed parts prepared by the tailor-welded parts obtained by the technical solution of the present invention have better high-speed deformation ability under the premise of ensuring quasi-static mechanical properties, absorb more energy during collisions, and have higher collision safety.
  • Example 1 0.15 1.2 4
  • Example 2 0.13 1.1 2.5
  • Example 3 0.15 1.9 4
  • Example 4 0.09 1.1 3.2
  • Example 5 0.14 1.9 3.1
  • Example 6 0.1 1.2 0.5 Example 7 0.09 1.9 4
  • Example 8 0.08 1.2 1.5
  • Example 9 0.15 1.8 2
  • Example 10 0.14 1.6 2.4
  • Example 11 0.05 1.9 4
  • Example 12 0.15 0.5 1.2
  • Example 13 0.15 0.5 2.6
  • Example 14 0.08 1.3
  • Example 15 0.12 1.9 1.8
  • Example 16 0.13 1.2 2.5
  • Example 17 0.12 1.6 3.2
  • Example 18 0.13 1.7 1
  • Example 19 0.15 0.7 0
  • Example 20 0.05 1.7 0.7
  • Example 21 0.13 1.38 3.0 Comparative example 1 - - - Comparative example 2 0.09 2.7 1.5
  • the weld structure of the tailored weldment obtained in Examples 1-21 is martensite + 1-15vol.% acicular ferrite dispersedly distributed + 0-5vol.% retained austenite, and the concentration of free aluminum in the weld is 0.1 ⁇ 4.0wt.%.
  • Tailored welded parts are hot stamped parts obtained by hot stamping forming process, so that a proper amount of dispersed ferrite in the weld seam of the hot stamped part is retained below, and the weld seam of the hot stamped part finally obtained
  • the structure is martensite + 0.1-10vol.% diffusely distributed acicular ferrite, iron-free aluminum intermetallic compound and massive ferrite.

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Abstract

一种钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件，采用带有铝或铝合金镀层（12、12'、22、22'）的待焊接钢板（10、20），通过调整焊接过程中的保护气（50）组分、焊丝（30）成分，结合焊接速度和送丝速度的控制，控制焊缝中的游离铝含量在0.1～4.0wt.％，防止拼焊过程中焊缝中生成铁铝金属间化合物，同时确保焊缝中生成适量弥散分布的铁素体。获得的拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体；经过热冲压成形得到的热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体。

Description

钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件 技术领域
本发明涉及焊接部件的制造方法，具体涉及一种钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件。
背景技术
轻量化、高强度的汽车钢板成为近年来汽车行业不断追求的目标，加之国家对于节能减排政策的大力推行，汽车行业对于汽车钢板的高强减薄的需求越来越多。热冲压技术相比于冷冲压技术具有减重效果明显、成形性好、尺寸精度高等优点，在汽车钢板实现高强化方面发挥着重要的作用。随着人们对于汽车的安全性、可靠性及舒适性要求的提高，众多车企从改善汽车结构设计和采用新的制造工艺等角度来提升产品质量。拼焊件是将几块相同/不同材质、相同/不同厚度或者相同/不同涂层的钢板焊接在一起，以实现零部件对材料性能的不同要求。激光拼焊件热冲压工艺一方面可以降低车体重量、提高装配精度简化装配步骤，同时可兼顾热冲压成形的优势，进一步提高钢板的成形性。
利用激光拼焊件形成的热冲压产品具有强度高、形状复杂、成形性好、尺寸精度高、回弹小等特点。热冲压用钢按照表面的状态可分为裸板和带镀层的钢板，在实际的热冲压过程中，裸钢表面容易在高温下产生氧化，形成氧化皮，在冲压过程中，氧化皮被挤压进入钢中，形成表面缺陷，大大影响其使用性能，带镀层的热冲压钢板相对于裸板可以在保护钢板不被氧化的同时省掉热冲压后的喷丸处理，因此，带有镀层的热冲压钢板受到越来越广泛的关注，目前常用的是铝或者铝合金镀层热冲压钢，但这种钢焊接时因镀层熔入熔池，形成脆而硬的金属间化合物(Fe 3Al、Fe 2Al 5、FeAl 3)及铁素体，致使焊接接头的强度、延性下降，无法使用。
中国专利CN101426612A公开了“由滚轧的涂镀板制造具有良好机械特性的焊接部件的方法”，该方法以含有铝硅镀层的钢板为原材料，制造只含金属间化合物为预涂层的焊接坯件，该方法解决了因铝熔入熔池使焊缝强度及延伸率不达标的问题，但钢板焊前需要对镀层进行消融处理，增加了设备投资，且使生产效率下降。
中国专利CN102985216A公开了“用含氮气和/或氧气的气体对镀铝钢部件的电弧/激光混合焊方法”，该专利中镀铝部件焊接时采用电弧+激光混合焊，保护气体加入附加气体氮气或氧气，附加气体体积含量为1～20％，附加气体的作用为捕获铝形成Al 2O 3或者AlN类的化合物，避免形成铁素体或其他有害的金属间化合物，形成的氧化铝或者氮化铝漂浮在熔池的表面，因此防止铝溶解在焊接熔池中(0015段)，焊缝组织为全马氏体组织。由该专利可知直接拼焊带铝或者铝合金镀层的钢板，焊接时因镀层侵入到熔池，使热冲压后焊接接头强度变差，接头的延率在1％左右，致使拼焊热成形部件在车辆碰撞时焊缝断裂，起不到应有的安全防护作用。
中国专利CN108025400A公开了“用于由具有铝基或铝硅基镀层的可淬火钢生产半成品板的激光焊接方法”，其针对差强热冲压钢板进行拼焊，最后得到的焊缝组织为全马氏体组织。
中国专利CN201380027064.4公开了“具有焊接凹口的金属板材件及其形成方法”，该方法以铝硅镀层钢板为原材料，将铝硅镀层全部去除后再焊接，该方法也可解决因铝熔入熔池使焊缝强度及延伸率不达标的问题，但镀层去除的深度控制难度高，因为如果镀层去除不完全，将与中国专利CN101426612A中公开的方法类似；如果镀层去除深度过大，将伤及钢基体，相当于材料变相减薄，焊后的接头性能必将降低；另外，镀层去除宽度的控制也是一个问题。去除宽度如果比焊缝窄，焊接时将有镀层元素熔入熔池，使焊缝性能下降；去除宽度如果比焊缝宽，则焊接热影响区将没有镀层保护，影响接头的耐蚀性。
中国专利CN104023899A公开的“拼焊件及其制造方法、以及使用拼焊件的热冲压部件”，该专利采用比母材碳、锰含量更高的焊丝对铝或者铝合金镀层板 进行焊接；虽然解决了焊缝性能问题，但其焊缝在热冲压时焊缝组织全部转变为马氏体，焊丝中的碳、锰含量比母材分别高0.1～0.8wt.％、1.5～7.0wt.％。众所周知，热冲压钢的碳、锰等元素的含量本身就很高，因此专利公开的焊丝是一种高碳高锰的焊丝，焊丝的制造难度高。
中国专利CN111230301A公开的“带铝或铝合金镀层的钢制薄壁焊接等强部件的制造方法”，该专利采用比母材碳、锰含量低的焊丝焊接1500MPa级铝或者铝合金镀层板，采用该方法所获得的焊接接头仅能达到1500MPa级别，使用该方法获得更高强度级别的热冲压部件，热冲压部件的焊接接头准静态拉伸时因焊缝强度低于母材，导致焊缝断裂，车厂无法使用。
发明内容
本发明目的在于提供一种钢制薄壁拼焊件的制造方法及使用该拼焊件制备的热冲压部件，解决拼焊过程中因镀层熔入熔池，导致拼焊件在热冲压后焊缝性能变差的问题，确保使用该拼焊件获得的热冲压部件焊接接头准静态拉伸断裂位置位于母材，接头延伸率大于4％，焊缝强度大于低强度母材抗拉强度；焊接接头在应变速率为40～800/s时，其拉伸断裂应变值大于0.08，更好地满足汽车生产领域的应用要求。
为达到上述目的，本发明的技术方案是：
一种钢制薄壁拼焊件的制造方法，其包括如下步骤：
1)钢板焊前准备
取两块强度级别相同或不同的待焊接钢板，焊前对待焊接钢板进行表面清洁，所述待焊接钢板包括基体及其至少一个表面上的铝或铝合金镀层，所述镀层包括与所述基体接触的金属间化合物合金层及其上的金属合金层，所述待焊接钢板的镀层不做去除或减薄处理；
2)焊接预置对接间隙
将待焊接钢板的对接间隙预置为0.1～0.5mm；
3)焊接工艺
采用激光填丝焊、熔化极活性气体保护电弧焊(Metal Active Gas Arc Welding，MAG焊)或激光MAG复合焊进行焊接；
其中，激光填丝焊中焊接速度为40～120mm/s，送丝速度为2～8m/min；
MAG焊的焊接速度为300～800mm/min；
激光MAG复合焊的焊接速度为40～150mm/s，送丝速度为2～10m/min；
保护气体为Ar+15～80vol.％CO 2+1～10vol.％N 2，保护气体流量为10～25L/min；
所述焊接用焊丝的成分中包括C、Mn、Ni奥氏体稳定化元素，焊丝成分中三种元素的含量减去待焊接钢板A中对应元素的含量，所得差值分别用△C、△Mn、△Ni表示；所述待焊接钢板A为强度级别相同的两块待焊接钢板中的其中之一，或强度级别不同的两块待焊接钢板中强度级别较低的待焊接钢板；其中，
待焊接钢板A的抗拉强度<900MPa，△C：-0.05～0.09wt.％，△Mn：-0.5wt.％～1.4wt.％，△Ni：0～4.0wt.％；或
900MPa≤待焊接钢板A的抗拉强度＜1300MPa，△C：-0.1～0.09wt.％，△Mn：-2～1.4wt.％，△Ni：0～4.0wt％；或
1300MPa≤待焊接钢板A的抗拉强度<1700MPa，△C：-0.21～-0.05wt.％，△Mn：-1.4～1.4wt.％，△Ni：1.76～4.0wt％；或
待焊接钢板A的抗拉强度≥1700MPa，△C：-0.26～-0.15wt.％，△Mn：-1.4～0.7wt.％，△Ni：2.26～4.0wt％；
所述拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体；焊缝中的游离铝含量为0.1～4.0wt.％。
优选的，步骤3)中，所述保护气体中CO 2含量为15～50vol.％。
优选的，步骤3)中，所述保护气体中N 2含量为2～4vol.％。
优选的，步骤3)中，所述MAG焊或激光MAG复合焊的焊接电流为110～130A，焊接电压为18～25V。优选的，步骤3)中，所述MAG焊或激光MAG复合焊的焊接电流为110～125A，焊接电压为18～25V。
优选的，步骤3)中，激光MAG复合焊的焊接速度为60～150mm/s，送丝速度为4～10m/min。
优选的，步骤3)中，所述激光填丝焊或激光MAG复合焊工艺中离焦量为-10～10mm，激光功率控制范围3～8kW。优选的，离焦量为-8～8mm，激光功率控制范围4～8kW。
优选的，步骤3)所述激光填丝焊或激光MAG复合焊工艺中，激光加工头可输出的最小光斑直径为0.3～1.6mm。本文中，本领域技术人员可根据实际情况选择相关参数，以保证激光加工头输出的最小光斑直径为0.3～1.6mm。例如，可设置聚焦镜的焦距与准直镜的焦距比值为0.75～4.0，瑞利长度(Rayleigh Length)为1.249～44.955，激光器传输光纤的直径为0.2～0.8mm，聚焦角(Focusing Angle)为2.3～18.4Grad。
优选的，步骤3)中，所述焊接为激光填丝焊，焊接速度为40～120mm/s，送丝速度为2～8m/min，离焦量为-8～8mm，激光功率控制范围4～8kW。
优选的，步骤3)中，所述焊接为MAG焊，焊接速度为400～800mm/min，焊接电流为110～125A，焊接电压为18～25V。
优选的，步骤3)中，所述焊接为激光MAG复合焊，焊接速度为60～150mm/s，送丝速度为4～10m/min，离焦量为-10～10mm，激光功率控制范围3～8kW，焊接电流为110～130A，焊接电压为18～25V。
优选的，所述焊接用焊丝的直径为1.0～1.6mm。
优选的，所述基体的厚度为0.5～3mm。
优选的，所述镀层为铝合金镀层，所述铝合金镀层的成分按重量百分比为：Si：5～11％，Fe：0～4％，其余量为Al及其它不可避免的杂质。在一些实施方案中，所述铝合金镀层的成分按重量百分比为：Si：8.5～10.5％，Fe：1.5～2.5％，其余量为Al及其它不可避免的杂质。
优选的，所述待焊接钢板A的抗拉强度<900MPa，其成分重量百分比为：C：0.06～0.1％，0＜Si≤0.1％，Mn：0.5～1.0％，P<0.03％，S<0.01％，Al<0.1％，0＜Cr≤0.1％，0＜Ti≤0.05％，其余为Fe及其它不可避免的杂质。
优选的，所述待焊接钢板A的抗拉强度大于等于900MPa小于1300MPa，其成分重量百分比为：C：0.06～0.15％，Si：0.3～1.0％，Mn：0.5～2.5％，P≤0.10％， S≤0.05％，Al：0.02～0.30％，Cr：0.05～0.5％，Nb：0.02～0.20％，V≤0.15％，Ti：0.01～0.10％，Mo≤0.5％，Ni≤0.5％，B：0.001～0.01％，余量为Fe及其它不可避免的杂质。
优选的，所述待焊接钢板A的抗拉强度大于等于1300MPa小于1700MPa，其成分重量百分比为：C：0.2～0.3％，Si：0.1～0.5％，Mn：0.5～2.5％，P<0.015％，S<0.05％，Al<0.1％，Ti<0.2％，B：0.0005～0.08％，Cr：0.01～1％，Ni≤0.24％，余量为Fe及其它不可避免的杂质。
优选的，所述待焊接钢板A的抗拉强度≥1700MPa，其成分按重量百分比为：C：0.30～0.39％，Si：0.05～0.6％，Mn：0.5～2.5％，P≤0.015％，S≤0.01％，Al：0.01～0.07％，Cr≤1.0％，Nb≤0.08％，V≤0.1％，Ti：0.01～0.12％，Mo：0.01～0.5％，Ni＜0.25％，B：0.0001～0.005％，N≤0.006％，余量为Fe及其它不可避免的杂质。
优选的，所述焊丝的成分按重量百分比为：C：0.05～0.15％，Mn：0.5～1.9％，Ni：0～4％，余量为Fe及其它不可避免的杂质。在一些实施方案中，焊丝中Ni的含量为0.5～4％。应理解，焊丝中C、Mn和Ni含量的选择需满足前文所述的要求。
本发明包括采用上述制造方法获得的钢制薄壁拼焊件。
在一些实施方案中，本发明提供一种钢制薄壁拼焊件，由两块强度级别相同或不同的待焊接钢板焊接而成，所述待焊接钢板包括基体及其至少一个表面上的铝或铝合金镀层，所述镀层包括与所述基体接触的金属间化合物合金层及其上的金属合金层，所述钢制薄壁拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体，焊缝中的游离铝含量为0.1～4.0wt.％。
优选的，所述基体的厚度为0.5～3mm。
优选的，所述镀层为铝合金镀层，所述铝合金镀层的成分按重量百分比为：Si：5～11％，Fe：0～4％，其余量为Al及其它不可避免的杂质。在一些实施方案中，所述铝合金镀层的成分按重量百分比为：Si：8.5～10.5％，Fe：1.5～2.5％，其余量为Al及其它不可避免的杂质。
优选的，所述两块待焊接钢板各自独立选自以下钢板：
抗拉强度<900MPa的钢板，其成分重量百分比为：C：0.06～0.1％，0＜Si≤0.1％，Mn：0.5～1.0％，P<0.03％，S<0.01％，Al<0.1％，0＜Cr≤0.1％，0＜Ti≤0.05％，其余为Fe及其它不可避免的杂质；
抗拉强度大于等于900MPa小于1300MPa的钢板，其成分重量百分比为：C：0.06～0.15％，Si：0.3～1.0％，Mn：0.5～2.5％，P≤0.10％，S≤0.05％，Al：0.02～0.30％，Cr：0.05～0.5％，Nb：0.02～0.20％，V≤0.15％，Ti：0.01～0.10％，Mo≤0.5％，Ni≤0.5％，B：0.001～0.01％，余量为Fe及其它不可避免的杂质；
抗拉强度大于等于1300MPa小于1700MPa的钢板，其成分重量百分比为：C：0.2～0.3％，Si：0.1～0.5％，Mn：0.5～2.5％，P<0.015％，S<0.05％，Al<0.1％，Ti<0.2％，B：0.0005～0.08％，Cr：0.01～1％，Ni≤0.24％，余量为Fe及其它不可避免的杂质；和
抗拉强度≥1700MPa的钢板，其成分按重量百分比为：C：0.30～0.39％，Si：0.05～0.6％，Mn：0.5～2.5％，P≤0.015％，S≤0.01％，Al：0.01～0.07％，Cr≤1.0％，Nb≤0.08％，V≤0.1％，Ti：0.01～0.12％，Mo：0.01～0.5％，Ni＜0.25％，B：0.0001～0.005％，N≤0.006％，余量为Fe及其它不可避免的杂质。
优选的，所述钢制薄壁拼焊件的焊缝组织中无铁铝金属间化合物及块状铁素体。
本发明还提供一种采用上述制造方法获得的钢制薄壁拼焊件制备得到的热冲压部件，该热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体，热冲压部件准静态拉伸断裂位置为母材，接头延伸率不低于4％；焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.08。
优选的，本发明所述热冲压部件的焊缝组织中铁素体含量为0.5～5vol.％。
优选的，本发明所述热冲压部件的焊缝组织中铁素体呈针状。
优选的，本发明所述热冲压部件的焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.09。
优选的，本发明所述热冲压部件的焊缝组织中无铁铝金属间化合物及块状铁素体。
本发明还提供一种热冲压部件，该热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体，热冲压部件准静态拉伸断裂位置为母材，接头延伸率不低于4％；焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.08。
优选的，所述热冲压部件采用本发明的钢制薄壁拼焊件制备得到，或采用本发明所述的制造方法获得的钢制薄壁拼焊件制备得到。
优选的，本发明所述热冲压部件的焊缝组织中铁素体含量为0.5～5vol.％。
优选的，本发明所述热冲压部件的焊缝组织中铁素体呈针状。
优选的，本发明所述热冲压部件的焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.09。
优选的，本发明所述热冲压部件的焊缝组织中无铁铝金属间化合物及块状铁素体。
本发明还提供一种制备热冲压部件的方法，所述方法包括对本发明的钢制薄壁拼焊件进行热冲压淬火的步骤。
在一些实施方案中，焊后对拼焊板进行热冲压淬火，加热温度为920～950℃，加热时间为3～6分钟，在通水模具中保压8～20秒钟。
优选的，所述方法包括采用本文任一实施方案所述的制造钢制薄壁拼焊件的方法制造钢制薄壁拼焊件的步骤，以及对所制造得到的钢制薄壁拼焊件进行热冲压淬火的步骤。
优选的，所述热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体，热冲压部件的焊接接头准静态拉伸断裂位置为母材，接头延伸率不低于4％；焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.08。
优选的，所述热冲压部件的焊缝组织中铁素体含量为0.5～5vol.％。
优选的，所述热冲压部件的焊缝组织中铁素体呈针状。
优选的，所述热冲压部件的焊缝组织中无铁铝金属间化合物及块状铁素体。
优选的，所述热冲压部件的焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.09。
本发明待焊接钢板选用的基体表面至少一个面上有镀层，在焊前、焊接过程中对待焊接钢板待焊区的镀层不做去除或减薄处理，由于含铝镀层的存在，因镀层熔入熔池，形成脆而硬的金属间化合物(Fe 3Al、Fe 2Al 5、FeAl 3)及过量铁素体，致使热冲压后的焊接接头的强度、延性下降，无法使用，为了提高拼焊件热冲压后的焊缝性能，焊接过程中应控制焊缝中游离铝的量，避免焊缝中形成铁铝金属间化合物的同时生成适量的铁素体。
焊接过程中使用氩气、二氧化碳和氮气混合的三元保护气体，N 2的体积含量为1～10％，N 2可以向焊缝中过渡氮元素，一方面，熔池中Al与N反应，形成的AlN随熔池剧烈搅拌而弥散分布在熔池中，经热冲压后将作为二次相粒子提高焊缝的强度；另一方面，熔池中的游离Al与N结合生成AlN，控制熔池中游离的Al浓度，防止过量铁素体的析出，同时也避免室温时焊缝中无铁素体。但保护气中N 2的比例不能过高，否则焊接接头的延性会降低，同时还会引发氮气孔。CO 2的体积含量为15～80％，CO 2增强了焊接区保护气体的活度，有利于增加板材的熔透率及液态金属的流动性，提高熔池金属的成分均匀性，规避铝元素的偏聚，保证焊缝成分均匀，规避因成分不均匀出现的条带组织，尤其是规避因铝聚集而形成的大块铁素体，确保铁素体弥散分布在焊缝中，使焊缝的性能稳定。
另外，焊接过程中使用的焊丝含有扩大奥氏体相区的碳、锰、镍等元素。控制焊缝中碳、锰、镍的元素含量与待焊接钢板之间的差值，一方面，这三个元素都是扩大奥氏体相区的元素，使高温铁素体区受到压缩，防止焊缝在热冲压模具闭合前析出过量铁素体，提高焊缝强度；另一方面，可降低焊缝的马氏体开始转变温度，保证马氏体的转化率。
碳是焊丝的重要组成元素，影响焊丝的可加工性及焊缝的碳当量。碳含量过低时，焊缝的奥氏体稳定性下降，难以保证焊缝的强度；碳含量过高时，焊丝的可制造性下降，焊缝的塑性和韧性下降。优选的，焊丝中C的含量可为0.05～0.15％。
锰作为焊丝的主要组成元素，可提高焊缝的奥氏体稳定性，使C曲线右移，从而降低马氏体临界冷却速率。锰含量过高，会影响焊丝的可制造性，焊缝的塑 性和韧性下降。Mn含量过低，焊缝的淬透性降低，强化作用减弱。优选的，焊丝中Mn的含量可为0.5～1.9％。
镍作为焊丝的另外一个主要组成元素，可增加焊缝中奥氏体的稳定性，降低临界Ms点温度，提高焊缝的淬透性、强度及韧性。镍含量过高，焊丝的生产成本会增加，且焊缝热冲压后的残余奥氏体会增加，影响焊缝的强度；焊丝的镍含量可以根据待焊板的强度级别进行调整，确保焊缝的强韧需求。优选的，焊丝中Ni的含量可为0～4％，如0.5～4％。
本发明中焊接用焊丝成分是基于低强钢级别待焊接钢板的成分而变化的，对于不同强度级别的待焊接钢板，焊丝成分可以相应变化，对应的焊缝成分也必然变化，即使焊后或热冲压后焊缝的组织一样，但焊缝所表现出来的力学性能是不同的，从而满足汽车行业对不同强度拼焊板的性能要求。
本发明在控制保护气体及焊丝成分的基础上，进一步控制焊接速度和送丝速度，改变焊缝中熔敷金属(焊丝熔化后形成的焊缝金属)的比例，尽管待焊接钢板含有铝或铝合金镀层，但拼焊件的焊缝中熔入的铝元素浓度是可以控制的。通过保护气、焊丝的成分及焊接工艺的共同作用，使拼焊件焊缝中游离铝的浓度控制在0.1～4.0wt.％。
众所周知，Al是铁素体形成的促进元素，减少焊缝中的游离Al，铁素体形成的能力就会减弱，将焊缝中游离Al的含量控制在0.1～4.0wt.％，一方面避免了焊缝生成过量的铁素体，保证了焊缝强度；另一方面可以避免焊缝中生成铁铝金属间化合物，且使适量的铁素体被保留在焊缝中，确保室温下拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体。
本发明拼焊件生产过程中重点调控拼焊件的焊缝组织构成，主要是调控铁素体的数量及形态，焊接过程中规避铁铝金属间化合物及块状铁素体生成，最终获得的拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体，拼焊件经热冲压成形工艺获得热冲压部件，使热冲压部件的焊缝中有适量弥散分布的铁素体被保留下面，最终获得的热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体。
本发明热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体，提高了焊接接头高速拉伸性能，应变速率为40～800/s时，焊接接头断裂应变值大于0.08。而传统的热冲压部件焊缝组织为单一马氏体，应变速率为40/s时，焊接接头断裂应变值在0.07左右；应变速率为800/s时，焊接接头断裂应变值在0.058左右，因此可知本发明热冲压部件高速拉伸断裂应变值显著提高。这是因为，马氏体的力学特点是强度高硬度高，变形能力差；铁素体的力学特点是塑性韧性好，变形能力强。焊缝组织为马氏体+弥散分布的针状铁素体的焊接接头相较焊缝组织为单一马氏体的焊接接头，在受到外力时可以为马氏体提供更多的协调变形机会；另外，马氏体的亚结构主要是位错，而铁素体的存在，会使焊缝组织中马氏体内部位错密度较焊缝组织为单一马氏体的有大幅下降；位错堆积易形成微裂纹，所以焊缝组织为马氏体+弥散分布的针状铁素体的焊接接头较焊缝组织为单一马氏体的焊接接头形成微裂纹的风险会大幅度下降；即使形成了微裂纹，弥散分布的铁素体对微裂纹的进一步长大、扩展也具有阻碍作用，从而使焊缝组织为马氏体+弥散分布的针状铁素体的焊接接头比焊缝组织为单一马氏体的焊接接头展现出更好的变形能力，尤其是在高速拉伸过程中。
这说明通过本发明技术方案获得的拼焊件，经过热冲压制备的热冲压部件在碰撞时，焊缝的变形能力更强，可吸收更多的能量，部件的碰撞安全性更高。但是热冲压部件焊缝中的铁素体含量不能太高，否则会降低焊缝的强度与韧性。
将热成形钢板进行拼焊，通过焊丝成分、焊接工艺及保护气的相互配合、相互支撑，增强热冲压后焊缝的强度，确保拼焊件经热冲压成形得到的热冲压部件焊接接头准静态拉伸断裂位置为母材，焊缝强度大于接头中低强钢的母材强度，且具有良好的高速拉伸性能，满足汽车生产领域的要求。
本发明的有益效果：
本发明采用带有铝或铝合金镀层的热冲压钢板进行拼焊，通过调整焊丝成分，控制焊接速度和送丝速度，保护气体采用三元保护气，减少拼焊件焊缝中游离铝的量，焊缝中游离铝含量控制在0.1～4.0wt.％，一方面避免了焊缝中生成过量的铁素体，保证了焊缝强度与韧性；另一方面可以避免焊缝中生成铁铝金属间化合物， 且使适量的铁素体被保留在焊缝中，保护气体中CO 2可以规避铝元素的偏聚，保证焊缝成分均匀，规避因铝聚集而形成大块铁素体，焊缝性能更加稳定。获得的拼焊件经过热冲压成形制备的热冲压部件，由于焊缝中存在AlN，焊缝强度进一步提升，焊接接头准静态拉伸断裂位置为母材，说明其焊缝强度大于母材强度，满足汽车生产领域的要求。
本发明通过焊丝成分、焊接工艺、保护气成分及含量的相互配合、相互支撑，确保拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体；这样拼焊件经热冲压成形后获得的热冲压部件的焊缝组织中形成马氏体+0.1～10vol.％弥散分布的铁素体，与焊缝组织为全马氏体的热冲压部件相比，本发明热冲压部件焊接接头高速拉伸性能得到明显提高，应变速率为40～800/s时，焊接接头断裂应变值大于0.08。而传统的热冲压部件焊缝组织为单一马氏体，应变速率为40/s时焊接接头断裂应变值在0.07左右，应变速率为800/s时焊接接头断裂应变值在0.058左右。即通过本发明技术方案获得的拼焊件制备的热成形部件在保证准静态力学性能的前提下，具有更优的高速变形能力，在碰撞时会吸收更多的能量，碰撞安全性更高。
附图说明
图1为本发明实施例1激光填丝拼焊示意图。
图2为本发明实施例1得到的热冲压部件焊接接头准静态拉伸性能曲线图。
图3为本发明实施例1得到的热冲压部件焊接接头准静态拉伸样断裂位置图。
图4为本发明实施例1得到的热冲压部件焊接接头金相图。
图5为本发明实施例1得到的热冲压部件焊接接头硬度分布。
具体实施方式
下面结合实施例和附图对本发明做进一步说明。本发明不局限于下面实施方式，任何人在本发明的启示下都可得出其它各种形式的产品，但不论在其形状或 结构上作任何变化，凡是具有与本申请相同或相近似的技术方案，均属于本发明的保护范围。
参见图1，本发明所述激光填丝拼焊，在保护气50的保护下，用激光束40熔化焊丝30及待焊接钢板10和待焊接钢板20实现拼焊；待焊接钢板10包括钢基体11及基体上的镀层12、12’，待焊接钢板20包括钢基体21及基体上的镀层22、22’，所述镀层是铝或者铝合金镀层。
表1所示为待焊接钢板10的成分，表2所示为待焊接钢板20的成分，表3为本发明所述焊丝的成分，表4所示为热冲压部件的焊接接头准静态拉伸性能，表5为热冲压部件的焊接接头高速拉伸性能。
本发明所述的钢制薄壁拼焊件的制造方法，包括如下步骤：
1)钢板焊前准备
取两块强度级别相同或不同的待焊接钢板，焊前对待焊接钢板进行表面清洁；
2)焊接预置对接间隙
将待焊接钢板的对接间隙预置为0.1～0.5mm；
3)焊接工艺
采用激光填丝焊、MAG焊或激光MAG复合焊，对两块待焊接钢板进行焊接。
实施例1-21和对比例1-2涉及到的待焊接钢板的铝合金镀层中Si与Fe成分的重量百分比见表1及表2，其余量为Al及其它不可避免的杂质；
实施例1-21和对比例1-2涉及到的强度级别500MPa、1000MPa、1500MPa和1800MPa指待焊接钢板热冲压后的抗拉强度级别。这4种强度级别对应的抗拉强度(按ISO 6892标准测试)范围分别为：500MPa级为400～750MPa，1000MPa级为1000～1300MPa，1500MPa级为1300～1700MPa，1800MPa级为1700～2150MPa。
实施例1
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.8mm，钢板成分见表1)、待焊接钢板20(强度级别为1800MPa，厚度t＝1.4mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率4kW，焊接速度80mm/s，离焦量10mm，送丝速度为4m/min，焊丝直径1.2mm，保护气体为48vol.％Ar+50vol.％CO 2+2vol.％N 2，气体流量为15L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后对拼焊板进行热冲压淬火，加热温度为945℃，加热时间为4分钟，在通水模具中保压10秒钟。
经过上述热循环，将拼焊板首先奥氏体化，在此加热期间镀层与钢中的原子相互扩展，使原有镀层全部转变为金属间化合物层，且该层厚度比原镀层厚度更厚。另外，该层具有高熔点、高硬度的特征，防止了基板在加热阶段、保压阶段被氧化和脱碳。在模具中保压期间，拼焊板发生马氏体转变。
焊接接头准静态拉伸曲线见图2，从图2可以看出热冲压部件的延伸率均大于4％，接头强度满足车厂要求。
接头断裂部位见图3，从图3可以看出热冲压部件焊接接头准静态拉伸时，断裂位置在母材上。
接头金相照片见图4，焊缝组织为马氏体+4.9vol.％弥散分布的针状铁素体，未见铁铝金属间化合物及块状铁素体。
接头硬度见图5，从图5上可以看出热冲压部件的焊缝与母材的硬度一致性较好。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例2
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.4mm，钢板成分见表1)、待焊接钢板20(强度级别为1800MPa，厚度t＝1.2mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.1mm，焊接功率3kW，焊接速度40mm/s，离焦量0mm，送丝速度为2m/min，焊丝直径1.0mm，保护气体为81vol.％Ar+15vol.％CO 2+4vol.％N 2，气体流量为10L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例3
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.8mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.6mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.5mm，焊接功率7kW，焊接速度50mm/s，离焦量-10mm，送丝速度为8m/min，焊丝直径1.2mm，保护气体为10vol.％Ar+80vol.％CO 2+10vol.％N 2，气体流量为25L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例4
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.2mm，钢板成分见表1)待焊接钢板20(强度级别为1500MPa，厚度t＝1.2mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.4mm，焊接功率4.5kW，焊接速度60mm/s，离焦量5mm，送丝速度为5m/min，焊丝直径1.2mm，保护气体为19vol.％Ar+80vol.％CO 2+1vol.％N 2，气体流量为20L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例5
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1000MPa，厚度t＝1.8mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.5mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.2mm，焊接功率5kW，焊接速度70mm/s，离焦量7mm，送丝速度为4m/min，焊丝直径1.2mm，保护气体为49vol.％Ar+50vol.％CO 2+1vol.％N 2，气体流量为17L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例6
对用于待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1000MPa，厚度t＝2.0mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.5mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.1mm，焊接功率5kW，焊接速度120mm/s，离焦量-5mm，送丝速度为7m/min，焊丝直径1.0mm，保护气体为40vol.％Ar+50vol.％CO 2+10vol.％N 2，气体流量为22L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例7
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为500MPa，厚度t＝1.6mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.4mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率8kW，焊接速度100mm/s，离焦量-8mm，送丝速度为6m/min，焊丝直径1.2mm，保护气体为46vol.％Ar+50vol.％CO 2+4vol.％N 2，气体流量为19L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例8
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为500MPa，厚度t＝1.4mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.2mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率5kW，焊接速度90mm/s，离焦量-6mm，送丝速度为5m/min，焊丝直径1.2mm，保护气体为83vol.％Ar+15vol.％CO 2+2vol.％N 2，气体流量为21L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例9
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.8mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.4mm，焊接功率8kW，焊接速度100mm/s，离焦量3mm，送丝速度为3m/min，焊丝直径1.6mm，保护气体为81vol.％Ar+18vol.％CO 2+1vol.％N 2，气体流量为23L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例10
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.75mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率8kW，焊接速度88mm/s，离焦量-3mm，送丝速度为5m/min，焊丝直径1.2mm，保护气体为74vol.％Ar+16vol.％CO 2+10vol.％N 2，气体流量为18L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例11
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.4mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.4mm，焊接功率5.5kW，焊接速度80mm/s，离焦量-6mm，送丝速度为5.5m/min，焊丝直径1.2mm，保护气体为58vol.％Ar+40vol.％CO 2+2vol.％N 2，气体流量为17L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例12
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.6mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.35mm，焊接功率7.5kW，焊接速度110mm/s，离焦量-7.5mm，送丝速度为7.5m/min，焊丝直径1.4mm，保护气体为51vol.％Ar+45vol.％CO 2+4vol.％N 2，气体流量为19L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例13
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.7mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.25mm，焊接功率6.5kW，焊接速度85mm/s，离焦量-5.5mm，送丝速度为5.5m/min，焊丝直径1.2mm，保护气体为65vol.％Ar+30vol.％CO 2+5vol.％N 2，气体流量为12L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例14
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1800MPa，厚度t＝1.4mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.8mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率7.5kW，焊接速度105mm/s，离焦量-4.5mm，送丝速度为8m/min，焊丝直径1.0mm，保护气体为59vol.％Ar+35vol.％CO 2+6vol.％N 2，气体流量为14L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例15
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.5mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.35mm，焊接功率4.5kW，焊接速度65mm/s，离焦量-7mm，送丝速度为4.5m/min，焊丝直径1.2mm，保护气体为67vol.％Ar+25vol.％CO 2+8vol.％N 2，气体流量为11L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例16
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为1000MPa，厚度t＝1.8mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.2mm，焊接功率5.5kW，焊接速度70mm/s，离焦量-6.5mm，送丝速度为5m/min，焊丝直径1.2mm，保护气体为73vol.％Ar+20vol.％CO 2+7vol.％N 2，气体流量为16L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例17
对待焊接的热成型钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.4mm，钢板成分见表2)采用如下工艺进行熔化极活性气体保护电弧拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.4mm；焊接电流为110A，焊接电压为22V，焊接速度500mm/min，焊丝直径1.2mm，保护气体为76vol.％Ar+20vol.％CO 2+4vol.％N 2，气体流量为13L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例18
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.7mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率4kW，焊接速度60mm/s，离焦量-6.5mm，送丝速度为4m/min，焊丝直径1.2mm，保护气体为56vol.％Ar+35vol.％CO 2+9vol.％N 2，气体流量为20L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例19
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1000MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.3mm，钢板成分见表2)采用如下工艺进行激光MAG复合拼焊，采用本发明所述焊丝(焊丝成分见表3)，焊接功率3kW，焊接速度80mm/s，拼接板间隙预留0.3mm，离焦量2mm；MAG热源的电流为120A，电压为20V；送丝速度为6m/min，焊丝直径1.2mm；保护气体为78vol.％Ar+20vol.％CO 2+2vol.％N 2，气体流量为24L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例20
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1000MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为500MPa，厚度t＝1.5mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.1mm，焊接功率5kW，焊接速度85mm/s，离焦量-8.5mm，送丝速度为6m/min，焊丝直径1.0mm，保护气体为40vol.％Ar+50vol.％CO 2+10vol.％N 2，气体流量为25L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
实施例21
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.2mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表2)采用如下工艺进行激光填丝拼焊，采用本发明所述焊丝(焊丝成分见表3)，拼接板间隙预留0.3mm，焊接功率5kW，焊接速度83mm/s，离焦量-6mm，送丝速度为7m/min，焊丝直径1.2mm，保护气体为40vol.％Ar+50vol.％CO 2+10vol.％N 2，气体流量为19L/min。
焊后对焊缝进行截面金相观察，焊缝宏观形貌优良，无明显飞溅。
焊后采用与实施例1相同的热冲压工艺进行热冲压。热冲压部件的焊接接头准静态拉伸性能见表4。热冲压部件的焊接接头高速拉伸性能见表5。
对比例1
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表2)采用消融焊进行拼焊。焊后采用与实施例1相同的热冲压工艺进行热冲压。采用消融焊获得的热冲压部件的焊缝组织为全马氏体。制备的拼焊热冲压件的高速拉伸试验结果见表5，试验参照标准ISO/DIS 26203-2执行。
对比例2
对待焊接的热成形钢板进行表面清理，去除表面的油污、水渍等污染物，确保表面清洁。
对带铝合金镀层的热冲压待焊接钢板10(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表1)、待焊接钢板20(强度级别为1500MPa，厚度t＝1.5mm，钢板成分见表2)，采用填丝焊进行焊接(焊丝成分见表3)，获得的热冲压部件的焊缝组织为马氏体+块状铁素体。焊接接头的高速拉伸试验结果见表5，试验参照标准ISO/DIS 26203-2执行。
由表4和表5可知，本发明获得的热冲压部件焊接接头准静态拉伸断裂位置为母材，说明其焊缝强度大于低强度母材强度，满足汽车生产领域的要求。其焊接接头高速拉伸性能得到明显提高，应变速率为40～800/s时，焊接接头断裂应变值大于0.09。
对比例1中采用传统的消融焊进行焊接，获得焊接接头的焊缝组织为单一马氏体，其应变速率为40/s时焊接接头断裂应变值在0.07左右，应变速率为800/s时焊接接头断裂应变值在0.058左右。
对比例2中虽然采用填丝焊进行焊接，但是焊丝成分不满足本发明要求，所以焊接接头断裂应变值最大值为0.029。即通过本发明技术方案获得的拼焊件制备的热成形部件在保证准静态力学性能的前提下，具有更优的高速变形能力，在碰撞时会吸收更多的能量，碰撞安全性更高。
表1 (单位：重量百分比)
Figure PCTCN2022114784-appb-000001
表2 (单位：重量百分比)
Figure PCTCN2022114784-appb-000002
Figure PCTCN2022114784-appb-000003
表3 (单位：重量百分比)
  C Mn Ni
实施例1 0.15 1.2 4
实施例2 0.13 1.1 2.5
实施例3 0.15 1.9 4
实施例4 0.09 1.1 3.2
实施例5 0.14 1.9 3.1
实施例6 0.1 1.2 0.5
实施例7 0.09 1.9 4
实施例8 0.08 1.2 1.5
实施例9 0.15 1.8 2
实施例10 0.14 1.6 2.4
实施例11 0.05 1.9 4
实施例12 0.15 0.5 1.2
实施例13 0.15 0.5 2.6
实施例14 0.08 1.3 1.3
实施例15 0.12 1.9 1.8
实施例16 0.13 1.2 2.5
实施例17 0.12 1.6 3.2
实施例18 0.13 1.7 1
实施例19 0.15 0.7 0
实施例20 0.05 1.7 0.7
实施例21 0.13 1.38 3.0
对比例1 - - -
对比例2 0.09 2.7 1.5
表4*
Figure PCTCN2022114784-appb-000004
Figure PCTCN2022114784-appb-000005
*接头准静态拉伸试验参照标准ISO 4136执行。
表5 *
Figure PCTCN2022114784-appb-000006
Figure PCTCN2022114784-appb-000007
*高速拉伸试验参照标准ISO/DIS 26203-2执行。
实施例1-21获得的拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的针状铁素体+0～5vol.％残余奥氏体，焊缝中游离铝的浓度为0.1～4.0wt.％，拼焊件经热冲压成形工艺获得热冲压部件，使热冲压部件的焊缝中有适量弥散分布的铁素体被保留下面，最终获得的热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的针状铁素体，无铁铝金属间化合物及块状铁素体。

Claims (15)

  1. 一种钢制薄壁拼焊件的制造方法，其特征是，包括如下步骤：
    1)钢板焊前准备
    取两块强度级别相同或不同的待焊接钢板，焊前对待焊接钢板进行表面清洁，所述待焊接钢板包括基体及其至少一个表面上有铝或铝合金镀层，所述镀层包括与所述基体接触的金属间化合物合金层及其上的金属合金层，所述待焊接钢板的镀层不做去除或减薄处理；
    2)焊接预置对接间隙
    将待焊接钢板的对接间隙预置为0.1～0.5mm；
    3)焊接
    采用激光填丝焊、MAG焊或激光MAG复合焊进行焊接；
    其中，激光填丝焊中焊接速度为40～120mm/s，送丝速度为2～8m/min；MAG焊的焊接速度为300～800mm/min；激光MAG复合焊的焊接速度为60～150mm/s，送丝速度为4～10m/min；
    保护气体为Ar+15～80vol.％CO 2+1～10vol.％N 2，保护气体流量为10～25L/min；
    焊接用焊丝的成分中C、Mn、Ni的含量减去待焊接钢板A中对应元素的含量，所得差值△C、△Mn、△Ni满足以下要求：
    待焊接钢板A的抗拉强度<900MPa，△C：-0.05～0.09wt.％，△Mn：-0.5～1.4wt.％，△Ni：0～4.0wt.％；或
    900MPa≤待焊接钢板A的抗拉强度＜1300MPa，△C：-0.1～0.09wt.％，△Mn：-2～1.4wt.％，△Ni：0～4.0wt％；或
    1300MPa≤待焊接钢板A的抗拉强度<1700MPa，△C：-0.21～-0.05wt.％，△Mn：-1.4～1.4wt.％，△Ni：1.76～4.0wt％；或
    待焊接钢板A的抗拉强度≥1700MPa，△C：-0.26～-0.15wt.％，△Mn：-1.4～0.7wt.％，△Ni：2.26～4.0wt％；
    其中，所述待焊接钢板A为强度级别相同的两块待焊接钢板中的其中之一，或强度级别不同的两块待焊接钢板中强度级别较低的待焊接钢板；
    其中，所述拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体；焊缝中的游离铝含量为0.1～4.0wt.％。
  2. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，步骤3)中，所述保护气体中CO 2含量为15～50vol.％。
  3. 如权利要求1或2所述的钢制薄壁拼焊件的制造方法，其特征是，步骤3)中，所述保护气体中N 2含量为2～4vol.％。
  4. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，所述MAG焊或激光MAG复合焊的焊接电流为110～130A，焊接电压为18～25V。
  5. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，所述激光填丝焊或激光MAG复合焊工艺中离焦量为-10～10mm，激光功率控制范围3～8kW；优选的，所述激光填丝焊或激光MAG复合焊工艺中，激光加工头输出的最小光斑直径为0.3～1.6mm。
  6. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，所述镀层为铝合金镀层，所述铝合金镀层的成分按重量百分比为：Si：5～11％，Fe：0～4％，其余量为Al及其它不可避免的杂质。
  7. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，
    所述待焊接钢板A的抗拉强度<900MPa，其成分重量百分比为：C：0.06～0.1％，0＜Si≤0.1％，Mn：0.5～1.0％，P<0.03％，S<0.01％，Al<0.1％，0＜Cr≤0.1％，0＜Ti≤0.05％，其余为Fe及其它不可避免的杂质；或
    所述待焊接钢板A的抗拉强度大于等于900MPa小于1300MPa，其成分重量百分比为：C：0.06～0.15％，Si：0.3～1.0％，Mn：0.5～2.5％，P≤0.10％，S≤0.05％，Al：0.02～0.30％，Cr：0.05～0.5％，Nb：0.02～0.20％，V≤0.15％，Ti：0.01～0.10％，Mo≤0.5％，Ni≤0.5％，B：0.001～0.01％，余量为Fe及其它不可避免的杂质；或
    所述待焊接钢板A的抗拉强度大于等于1300MPa小于1700MPa，其成分重量百分比为：C：0.2～0.3％，Si：0.1～0.5％，Mn：0.5～2.5％，P<0.015％，S<0.05％， Al<0.1％，Ti<0.2％，B：0.0005～0.08％，Cr：0.01～1％，Ni≤0.24％，余量为Fe及其它不可避免的杂质；或
    所述待焊接钢板A的抗拉强度≥1700MPa，其成分重量百分比为：C：0.30～0.39％，Si：0.05～0.6％，Mn：0.5～2.5％，P≤0.015％，S≤0.01％，Al：0.01～0.07％，Cr≤1.0％，Nb≤0.08％，V≤0.1％，Ti：0.01～0.12％，Mo：0.01～0.5％，Ni＜0.25％，B：0.0001～0.005％，N≤0.006％，余量为Fe及其它不可避免的杂质。
  8. 如权利要求1所述的钢制薄壁拼焊件的制造方法，其特征是，所述焊丝的成分按重量百分百为：C：0.05～0.15％，Mn：0.5～1.9％，Ni：0～4％、优选0.5～4％，余量为Fe及其它不可避免的杂质。
  9. 一种钢制薄壁拼焊件，其由两块强度级别相同或不同的待焊接钢板焊接而成，所述待焊接钢板包括基体及其至少一个表面上有铝或铝合金镀层，所述镀层包括与所述基体接触的金属间化合物合金层及其上的金属合金层，所述钢制薄壁拼焊件的焊缝组织为马氏体+1～15vol.％弥散分布的铁素体+0～5vol.％残余奥氏体，焊缝中的游离铝含量为0.1～4.0wt.％；优选地，所述制薄壁拼焊件采用权利要求1-8中任一项所述的方法制备得到。
  10. 一种热冲压部件，其特征是，所述热冲压部件的焊缝组织为马氏体+0.1～10vol.％弥散分布的铁素体，焊接接头准静态拉伸断裂位置为母材，接头延伸率不低于4％；焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.08。
  11. 如权利要求10所述的热冲压部件，其特征是，所述热冲压部件采用权利要求1-8中任一项所述的制造方法获得的钢制薄壁拼焊件制备得到，或采用权利要求9所述的钢制薄壁拼焊件制备得到。
  12. 如权利要求10所述的热冲压部件，其特征是，所述热冲压部件的焊缝组织中铁素体含量为0.5～5vol.％；和/或
    所述热冲压部件的焊缝组织中铁素体呈针状。
  13. 如权利要求10所述的热冲压部件，其特征是，所述热冲压部件的焊接接头在应变速率为40～800/s时，焊接接头拉伸断裂应变值大于0.09。
  14. 一种制造热冲压部件的方法，其特征是，该方法包括采用权利要求1-8中任一项所述的制造钢制薄壁拼焊件的方法制造钢制薄壁拼焊件的步骤，以及对所制造得到的钢制薄壁拼焊件进行热冲压淬火的步骤。
  15. 如权利要求14所述的方法，其特征是，所述热冲压淬火中，加热温度为920～950℃，加热时间为3～6分钟，在通水模具中保压8～20秒钟。
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