CN116372367A - Splice welding plate with aluminum-silicon coating and preparation method thereof - Google Patents
Splice welding plate with aluminum-silicon coating and preparation method thereof Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 229
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 title claims abstract description 70
- 238000000576 coating method Methods 0.000 title claims abstract description 69
- 239000011248 coating agent Substances 0.000 title claims abstract description 68
- 238000002360 preparation method Methods 0.000 title claims abstract description 7
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims abstract description 93
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 85
- 239000010959 steel Substances 0.000 claims abstract description 85
- 239000000945 filler Substances 0.000 claims abstract description 65
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 26
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 21
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 16
- 238000000034 method Methods 0.000 claims description 52
- 238000004519 manufacturing process Methods 0.000 claims description 27
- 229910052799 carbon Inorganic materials 0.000 claims description 26
- VNNRSPGTAMTISX-UHFFFAOYSA-N chromium nickel Chemical compound [Cr].[Ni] VNNRSPGTAMTISX-UHFFFAOYSA-N 0.000 claims description 19
- 238000001816 cooling Methods 0.000 claims description 13
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims description 8
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- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- KMWBBMXGHHLDKL-UHFFFAOYSA-N [AlH3].[Si] Chemical compound [AlH3].[Si] KMWBBMXGHHLDKL-UHFFFAOYSA-N 0.000 claims 1
- 238000005238 degreasing Methods 0.000 claims 1
- 239000011651 chromium Substances 0.000 abstract description 63
- 229910001566 austenite Inorganic materials 0.000 abstract description 27
- 239000011572 manganese Substances 0.000 abstract description 27
- 229910000734 martensite Inorganic materials 0.000 abstract description 20
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 abstract description 12
- 238000005516 engineering process Methods 0.000 abstract description 8
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- 230000000087 stabilizing effect Effects 0.000 abstract description 7
- 238000013461 design Methods 0.000 abstract description 4
- 238000011161 development Methods 0.000 abstract description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 abstract description 3
- 239000010953 base metal Substances 0.000 abstract description 3
- 239000007769 metal material Substances 0.000 abstract description 2
- WHROWQPBDAJSKH-UHFFFAOYSA-N [Mn].[Ni].[Cr] Chemical compound [Mn].[Ni].[Cr] WHROWQPBDAJSKH-UHFFFAOYSA-N 0.000 abstract 1
- 238000013329 compounding Methods 0.000 abstract 1
- 229910000859 α-Fe Inorganic materials 0.000 description 27
- 230000008569 process Effects 0.000 description 19
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- 238000010587 phase diagram Methods 0.000 description 14
- 210000001503 joint Anatomy 0.000 description 13
- 230000000171 quenching effect Effects 0.000 description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 10
- 239000000463 material Substances 0.000 description 10
- 238000011049 filling Methods 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 238000009776 industrial production Methods 0.000 description 7
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- 238000007747 plating Methods 0.000 description 5
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- AMWRITDGCCNYAT-UHFFFAOYSA-L hydroxy(oxo)manganese;manganese Chemical compound [Mn].O[Mn]=O.O[Mn]=O AMWRITDGCCNYAT-UHFFFAOYSA-L 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
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- 229910018125 Al-Si Inorganic materials 0.000 description 3
- 229910018520 Al—Si Inorganic materials 0.000 description 3
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- 229910001339 C alloy Inorganic materials 0.000 description 2
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 2
- VYPSYNLAJGMNEJ-UHFFFAOYSA-N Silicium dioxide Chemical compound O=[Si]=O VYPSYNLAJGMNEJ-UHFFFAOYSA-N 0.000 description 2
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- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 2
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- QMQXDJATSGGYDR-UHFFFAOYSA-N methylidyneiron Chemical compound [C].[Fe] QMQXDJATSGGYDR-UHFFFAOYSA-N 0.000 description 2
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- 241001391944 Commicarpus scandens Species 0.000 description 1
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- 238000003723 Smelting Methods 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- KCZFLPPCFOHPNI-UHFFFAOYSA-N alumane;iron Chemical compound [AlH3].[Fe] KCZFLPPCFOHPNI-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 1
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- 229910052758 niobium Inorganic materials 0.000 description 1
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Classifications
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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
- B23K26/20—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
- B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
- B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
- B23K35/24—Selection of soldering or welding materials proper
- B23K35/30—Selection of soldering or welding materials proper with the principal constituent melting at less than 1550 degrees C
- B23K35/3053—Fe as the principal constituent
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
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- Optics & Photonics (AREA)
- Mechanical Engineering (AREA)
- Plasma & Fusion (AREA)
- Laser Beam Processing (AREA)
Abstract
The invention belongs to the field of metal materials, and particularly relates to a splice welding plate with an aluminum-silicon coating and a preparation method thereof. The invention is based on the ternary alloying thought of chromium-nickel-manganese, the total amount of the aluminum-silicon coating entering into a welding seam is reduced without removing the coating or chamfering before welding, and the aluminum-silicon coating hot forming steel welding joint with excellent performance can be obtained by adopting conventional laser to carry out filler wire welding. The existing welding wire is mainly composed of austenite stabilizing elements, and the invention innovatively designs a welding wire component system. The welding wire is designed by adopting the idea of compounding non-austenite stabilizing elements of chromium, nickel and manganese according to a certain proportion, and the full martensite of the weld joint structure is realized by controlling the equivalent ratio of chromium to nickel of the welding wire. The invention aims to obtain the welded joint reaching the base metal level in a low-cost and high-efficiency mode, and has important significance for the development of the aluminum-silicon coated steel laser welding technology.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to a splice welding plate with an aluminum-silicon coating and a preparation method thereof.
Background
The high strength of steel for automobiles is a necessary trend in the development of automobile materials. However, it is difficult to manufacture parts by conventional cold stamping for high strength steels of 1000MPa or more, and hot stamping techniques have been developed. As is well known, hot stamping is a process of heating a steel sheet to 900 to 950 ℃ to heat-deform and quenching with dies to obtain a part of a desired shape. In order to avoid oxidation and decarburization of the surface of the steel plate in the hot forming process, a 30 mu m aluminum-silicon coating layer is often coated on the surface of the hot formed steel in advance, namely the aluminum-silicon coating layer hot formed steel.
In recent years, the welding together of aluminum-silicon plated hot formed steels of different thicknesses or different strengths to form a laser tailor-welded blank has received great attention and application because the laser tailor-welded blank can place the appropriate materials in the appropriate locations, maximizing the structural weight and weight savings. However, industrial applications and studies have found that the presence of a certain amount of ferrite causes a 30% decrease in the strength of the weld joint, as the aluminum-silicon coating enters the weld pool during laser welding, resulting in the weld joint not obtaining a fully martensitic structure.
In order to solve the problem of welding aluminum-silicon coating hot forming steel, industry and scholars try a plurality of methods, mainly comprising the following three methods:
firstly, removing the aluminum silicon coating in advance before welding. Although the method is one of the main technologies (CN 200780013854.1) applied in the current industrial production, the method needs to adopt another laser to remove the aluminum-silicon coating in advance before laser welding, obviously, the method increases the manufacturing procedures and equipment and also prolongs the manufacturing efficiency of the aluminum-silicon coating splice welding plate. Similarly, there are also techniques for removing the plating layer by plasma ablation (cn201810223902. X) and high-energy electron beam (CN 201810581119.0). With the trend of green and low cost of automobile manufacture, the method cannot be well adapted to future development.
Second, the adverse effect of aluminum on the weld is suppressed by optimizing the welding process. The scholars in this aspect mainly solve the adverse problem of aluminum by converting the Al-Si layer into an Al-Fe alloy layer through pretreatment before welding, or by promoting the uniform distribution of aluminum in a molten pool through pulse laser (CN 201910949005.1), or by stirring the molten pool through swinging of a laser beam to promote the uniform distribution of aluminum, or by controlling shielding gas in the laser welding process (CN 201180034151.3, CN 201611036496.3), or by double-beam laser welding (CN 201810507547.9). According to the method, the pre-welding pretreatment is still to add working procedures before welding, so that the process is more complicated than direct welding, and the cost is obviously increased; although the use of pulsed laser for welding can help the distribution of aluminum, the technology (CN 201910949005.1) clearly requires that the laser needs to be pulse-adjustable, obviously has higher requirements on the laser itself, and the use of pulsed laser will affect the welding speed, so that high-speed welding with a speed of more than 6m/min cannot be realized, which is not beneficial to improving efficiency in industrial production. The most direct problem of aluminum-silicon coating welding by adding proper oxidizing atmosphere into shielding gas is that oxygen reacts with aluminum and also reacts with beneficial elements such as iron, manganese, carbon and the like in steel, so that welding line element ablation and even welding line dishing are caused, that is, the welding line performance and welding line morphology cannot be controlled stably.
Thirdly, adoptThe solution is achieved by weld alloying. In the CN201611247493.4 patent, it is proposed to preform nickel foil or chromium foil in the weld during laser welding, or to add nickel wire or chromium wire to the weld using a wire feeder, and to use argon gas as shielding gas during welding, so that a weld of fully martensitic structure can be obtained. Although the method can solve the problem of the strength of the welded joint, the technology needs to use high-purity nickel or chromium (the purity reaches 90% -99.99%), obviously the welding seam alloying cost is very high, and moreover, the industrial production by adopting a prefabricated metal foil mode is very difficult and the forming quality of the welding seam cannot be controlled. The CN201810032131.6 patent discloses a method for manufacturing aluminum-silicon coating hot forming steel tailor-welded blank by using laser filler wire welding process, but the specific component design concept and element content of the welding wire are not disclosed in the patent, and only the required elements are required to be added. CN201911306466.3 discloses a flux and process for laser welding a surface-coated Al-Si hot formed steel, the binder (in mass percent (wt/%) being Silica (SiO) 2 ) 15-20%, manganese oxide (MnO) 20-30%, iron oxide (FeO) 10-15%, calcium fluoride (CaF) 2 ) 5-10%, cryolite (Na) 3 AlF 6 ) The balance) is coated at the welding position of the hot forming steel with the Al-Si coating on the surface, and then the flux is adhered to the surface coated with the adhesive at the welding position of the welding joint for welding, so that the performance of the welding joint is improved, but the method still needs to add a coating process before welding and additionally consumes adhesive materials. CN201380001259.1 also mentions that no ferrite is produced at 800-950 ℃ at the laser weld by filler wire, wherein the wire is specifically required to contain carbon or manganese, the filler wire carbon content being 0.1-0.8 higher than the carbon content of the base material (aluminum silicon plated hot formed steel) and the manganese content being 1.5-7.0 higher than the base material, i.e. carbon and manganese are used in this patent to control ferrite formation in the weld. CN201510165732.0 requires 0.6% -0.9% of c, 0.3% -0.9% of mn, 1.6% -3.0% of ni, and the balance iron in the welding wire for laser filler wire welding, and obviously, in this patent, austenitizing forming element carbon is used as a core element for controlling ferrite formation in the welding seam. CN201811424758 is also mentionedTo the welding wire used, a plurality of austenitizing elements of C, mn, ni and N are contained. CN201810032131.6 indicates that the welding wire needs to include an element rich in austenite and an element poor in ferrite. The welding wire for welding the aluminum silicon coated steel in the CN201680054858.3 patent comprises 0.5-1.5% of C, 0.5-2.0% of Si, 1.0-3.0% of Mn, 0.5-2.0% of Cr+Mo, 1.0-4.0% of Ni, and the balance of Fe and impurities. Although the method can solve the problem of the strength of the welded joint, the technology needs to be preheated to 100 ℃ by a heating device before filler wires are subjected to filler wire welding in the implementation process, which increases the difficulty and cost in industrial production. The filler wire of CN202010191741.8 patent uses Ni as the main element, and a weld joint of fully martensitic structure can be obtained. However, in the process, the plate gap in the assembly link is required, the thickness of the plate and the diameter of the welding wire are strictly matched according to the formula shown in the patent, the welding speed is only 1-2 m/min, the process is complex, and the production efficiency is required to be improved. Analytically, the above methods of filler wire welding are all too complex to implement, and the wire relies primarily on the addition of austenite forming elements to control ferrite formation.
The welding wire of the above patent is mostly controlled in weld structure by adding austenite forming elements, while the welding wire of the following two disclosures is added with chromium and other alloying elements. The welding wire composition used for welding the aluminum silicon coated steel in the CN202210625063.0 patent comprises 0.10-0.22 percent of C, 0.20-0.50 percent of Si, 2.0-3.5 percent of Mn, 3.0-7.0 percent of Ni, 2.0-3.0 percent of Cr, 0.020-0.030 percent of Nb and the balance of Fe and unavoidable impurities, but the Nb element is intentionally added in the welding wire to play roles of grain refinement and precipitation strengthening, thereby improving the strength and toughness, and naturally, the difficulty of component control and the smelting cost are additionally increased. Recently, a process for welding aluminum-silicon coated steel by using variable energy distribution laser spot filler wire is proposed in Laserweldingerplaserliblanksmadeof Al-Si-coated22MnB5steelusingafillerwire andavariableenergydistributionlaseroptics (DOI: 10.1007/s 00170-023-10921-4), wherein the components of the used welding wire are 0.05% -0.4% C, 0-3.0% Mn, 0-2.0% Si, 5% -12% Ni, 4% -25% Cr, 0-0.5% Mo, and the balance being iron. The alloy element molybdenum is added into the welding wire to refine grains.
In summary, the laser filler wire welding is adopted to realize the direct welding of the aluminum-silicon coating hot forming steel, but the core is the component system design of the welding wire, and the pretreatment such as grooving or preheating should not be carried out before welding, so that the welding cost is increased and the production efficiency is reduced. Therefore, in view of convenience, high efficiency and low cost of practical industrial production, a new welding wire composition system is designed and high-quality welding can be completed under conventional wire filling welding equipment and process.
Disclosure of Invention
The invention provides a brand new welding wire component system (instead of austenite forming elements such as nickel, manganese, carbon and the like, ferrite forming elements chromium are cooperatively used, and the final weld joint structure is ensured by controlling chromium-nickel equivalent), meanwhile, the steel plate does not need to be pretreated before welding, the laser used in the welding process is a common laser (no additional optical accessories are needed to be added to adjust the light spot energy distribution), and the manufacture of the aluminum-silicon coating tailor-welded blank can be completed without using protective gas. Compared with the thought of adopting pure nickel/pure chromium, the method obviously reduces the cost and improves the weld controllability, and compared with other welding wire design concepts, the method does not emphasize the increase of austenite forming elements and reduces ferrite forming elements, has simple welding process and easier implementation, and has the characteristics of stronger adaptability to industrial production and low cost.
In order to solve the technical problems, the application provides the following technical scheme: the invention provides a preparation method of a splice welding plate with an aluminum-silicon coating, which comprises the following steps:
s1: after purifying the hot-formed steel plates with the aluminum-silicon coating, placing the hot-formed steel plates at intervals to form gaps between the hot-formed steel plates with the aluminum-silicon coating;
s2: welding filler wires in the gaps by laser to obtain the splice welding plate with the aluminum-silicon coating; the filler wire comprises Fe, C, mn, cr, ni and a doping element, wherein the doping element is one or more of Si, al, P, S and N;
[ C ] in the filler wire]+[Mn]+[Cr]+[Ni]＝12～45％，[C]≤0.5％，[Mn]≤3％，[Ni]=7.5 to 25%, chromium-nickel equivalent Cr eq /Ni eq ≤1.2；
Wherein Cr is eq ＝1[Cr]+(1.3～1.8)[Si]+(5.3～5.8)[Al]+(0.10～0.15)[P]+(0.05～0.1)[S]，Ni eq ＝1[Ni]+(28～34)[C]+(27～31)[N]+(0.3～0.7)[Mn]The method comprises the steps of carrying out a first treatment on the surface of the In [ Cr ]]、[Si]、[Al]、[P]、[S]、[Ni]、[C]、[N]And [ Mn ]]The mass fraction of each element in the filler wire.
Because the specific value of the chromium-nickel equivalent of the weld joint structure is related to the Al content in the weld joint and the dilution rate of the welding wire, the value of the chromium-nickel equivalent of the weld joint structure can fluctuate with the change of the process conditions. The method adopts elements contained in the filler wire to establish a chromium-nickel equivalent criterion conforming to the filler wire, and the element front coefficient in the criterion represents the capability of the element to increase ferrite/austenite stability.
Preferably, in the filler wire, the content of Cr is 2-12% by mass fraction.
When the coating is mixed into the welding region and the Al content of the welding region increases, a complete austenite structure cannot be ensured even if the welding region is heated at a temperature of 900 to 950 ℃, and even if the welding portion is quenched after hot press forming, the welding portion has a structure in which ferrite and martensite coexist with each other instead of having a complete martensite structure. For this reason, deterioration of the strength of the welded portion is caused.
The increase of C element in the weld joint leads to the increase of the yield point, the hardness and the tensile strength of the weld joint structure, and the weld joint structure is used as an austenite stabilizing element to effectively inhibit ferrite formation, enlarge an austenite phase region and reduce the Ac3 (Ac 3 line of an iron-carbon alloy, which is generally between 727 and 912 ℃). When the content of the C element in the welding wire is too much, the welding wire is easy to break in the production process, which is unfavorable for mass production, and meanwhile, the welding seam embrittlement is easy to be caused by the too high content of the C element, so that the content of the C element is not more than 0.5wt%.
The Mn element has a solid solution strengthening effect by being solid-dissolved in ferrite and austenite. As an austenite stabilizing element, mn can expand the austenite phase region, improve the austenite structure stability, and suppress ferrite formation to lower the temperature Ac 3. Mn element can strongly reduce the martensite transformation temperature and strongly increase the hardenability of steel. The hardness and strength of the welding line are improved, the ductility of the welding line is not influenced, and the toughness is not obviously reduced. The excessive content of Mn element is easy to cause the segregation of weld joint components, and simultaneously, the austenite stability is easy to be too high and remain in a room-temperature weld joint structure. Therefore, it is not suitable to add a large amount of weld structure, and the composition range is set to not more than 3wt%.
The Ni element can be infinitely dissolved with Fe, and has strong functions of expanding an austenite phase region, reducing the transformation temperature of martensite and reducing the Ac3 temperature. The Ni element can improve the hardenability, the weld strength and fatigue performance, the atmospheric corrosion resistance and the toughness and the plasticity of the weld. According to experimental results, considering the change of welding parameters and dilution rate, when the Ni content in the welding wire is lower than 7.5wt%, ferrite in the welding seam can not be completely inhibited under the high-speed welding condition, and the welding seam can not obtain a full martensitic structure; when the Ni content in the welding wire is higher than 25wt%, the austenite stability is too high, residual austenite in the welding seam remains in a room temperature structure, and the mechanical property of the welding seam is reduced, so that the Ni content is set to be not more than 25wt%.
The filler wire contains C, mn and Ni as austenite stabilizing elements, suppresses ferrite precipitation in the welding region, enlarges the austenite phase region, causes the welding region to be heated and insulated at 900-950 ℃ to ensure that a complete austenite structure is obtained, and is quenched after hot stamping, and the welding region has a complete martensite structure. Meanwhile, C, mn and Ni contribute to the improvement of the hardness and strength of the weld zone. Within the composition range according to the invention, the weld region still has good plasticity.
The filler wire contains Cr alloy elements, even though it is shown by a great deal of researches by other scholars that Cr is a ferrite stabilizing element, adding Cr into the weld zone promotes precipitation of ferrite, which is disadvantageous to obtain a complete martensitic structure. But Cr element can improve the hardenability, the hardness and the strength of the weld, the oxidation resistance, the high-temperature oxidation resistance and the oxidation resistance medium corrosion, and simultaneously reduce the Ac3 temperature (Ac 3 line of the iron-carbon alloy, generally between 727 and 912 ℃), so that the weld zone is effectively promoted to obtain a complete martensitic structure, and the weld has good comprehensive mechanical properties after quenching. Cr can replace Ni to a certain extent, so that the Ni content in the welding wire is reduced, and the production cost of the welding wire is reduced.
The weld joint structure is a full martensitic structure when the chromium-nickel equivalent ratio of the welding wire is less than 1.20.
According to experimental results and simulation results, when Cr element and Ni element are mixed in a certain proportion for use, various material properties of a welding area cannot be changed obviously, meanwhile, when the welding area is quenched after hot stamping forming at 900-950 ℃, the Cr element can effectively inhibit precipitation of secondary ferrite, the Ac3 temperature is reduced, and meanwhile, the production cost of the welding wire is greatly reduced.
(1) Substitution of Ni by Cr
As shown in fig. 3 and 5-9, which are the equilibrium phase diagram and the quenching phase diagram of the weld joint, when the Ni content in the weld joint is 2.5wt%, the Ac3 temperature is 949 ℃ (less than 950 ℃), which meets the requirements; the simulation results show that there is still 1wt% ferrite left under the quenching condition of 950 ℃. When the Ni content is adjusted to be 2wt%, the Ac3 temperature breaks through 950 ℃ when the Cr content is not added, and the ferrite content under the quenching condition is up to 7.8wt%; when 2wt% Cr is added, ac3 temperature is reduced to 950 ℃ again, and a full martensitic structure is obtained under quenching conditions. This means that 2wt% of Cr is added to the weld structure while 0.5wt% of Ni is reduced, the equilibrium solidification path and structure of the weld structure are not changed, the Ac3 temperature is reduced, and a fully martensitic structure is more easily obtained under quenching conditions.
(2) Cr content should be varied with Ni content
Taking the weld joint structure Ni content of 2wt% as an example, as shown in figures 3 and 5-9, the Ac3 temperature of the weld joint structure is higher than 950 ℃, and 7.8wt% ferrite remains under the quenching condition. At this time, when the Cr content in the filler wire is less than 5wt%, ferrite residue cannot be completely eliminated, and a fully martensitic structure cannot be ensured under quenching conditions. When the Cr content is higher, the ferrite stability of the weld joint structure is increased, the austenite phase region is reduced, and the weld joint structure is also unfavorable for obtaining a full martensitic structure. Thus, for any given Ni content, there is a certain range of Cr content to Ni content, only within which the weld structure is guaranteed to be fully martensitic.
However, in the welding wire and the base material of the present invention, the elements affecting the stability of ferrite and austenite are not only Cr elements and Ni elements, so that it is not feasible to singly use the content ratio of Cr to Ni as a criterion. Therefore, the ratio of chromium and nickel equivalent is used as a criterion. Chromium equivalent Cr eq The values of (2) can represent the ability of each alloy element in the structure to form a ferrite structure, and the nickel equivalent Ni eq The values can represent the ability of the individual alloying elements in the structure to form an austenitic structure. The pre-element coefficient in the criterion represents the ability of the element to increase ferrite/austenite stability.
Preferably, the purification treatment method is to use acetone or ethanol to clean oil stains on the surface of the hot-formed steel plate with the aluminum-silicon coating, and then cool and air-dry the steel plate.
Preferably, the diameter of the filler wire is greater than the width of the gap.
Preferably, in the step S2, the filler wire is fed by a filler wire feeding device, and the feeding speed is 1-10 m/min.
Preferably, in the step S2, a laser used for the filler wire irradiates the butt joint of the hot-formed steel sheet.
Preferably, in the step S2, the power of the laser welding is 500-6000W, and the scanning speed is 1-10 m/min.
Preferably, in the step S2, the laser spot diameter of the laser welding is 0.03 to 2.00mm.
Preferably, in the step S2, the welding is performed in an atmospheric environment without a protective atmosphere.
The invention also provides the splice welding plate with the aluminum-silicon coating, which is prepared by the preparation method, and the microstructure structure of the welding joint on the splice welding plate with the aluminum-silicon coating is lath martensite.
The invention also provides a method for judging the welding quality of the splice welding plate with the aluminum-silicon coating, which comprises the following steps: detecting the components of Cr, si, al, P, S, ni, C, N and Mn in the welding wire during welding, and calculating the Cr-Ni equivalent Cr of the welding wire eq /Ni eq The method comprises the steps of carrying out a first treatment on the surface of the Wherein Cr is eq ＝1[Cr]+(1.3～1.8)[Si]+(5.3～5.8)[Al]+(0.10～0.15)[P]+(0.05～0.1)[S]，Ni eq ＝1[Ni]+(28～34)[C]+(27～31)[N]+(0.3～0.7)[Mn]，[Cr]、[Si]、[Al]、[P]、[S]、[Ni]、[C]、[N]And [ Mn ]]Cr, si, al, P, S, ni, C, N and Mn in the filler wire; if [ C ]]+[Mn]+[Cr]+[Ni]＝12～45％，[C]≤0.5％，[Mn]≤3％，[Ni]=7.5 to 25% and chromium-nickel equivalent Cr eq /Ni eq When the welding quality of the splice welding plate with the aluminum-silicon coating is less than or equal to 1.2, the welding quality of the splice welding plate with the aluminum-silicon coating is qualified; otherwise, the welding quality of the splice welding plate with the aluminum-silicon coating is unqualified.
The invention relates to an aluminum-silicon coating 22MnB5 welding joint prepared by adopting a laser filler wire welding technology based on a chromium-nickel alloying thought. Currently available welding wires consist mainly of austenite stabilizing elements. The invention innovates a welding wire component system. The welding wire is designed by adopting the idea that non-austenite stable element chromium and nickel are compounded according to a certain proportion. The purpose of the present invention is to obtain a welded joint that reaches the base material level in a cost-effective manner. The method has important significance for the development of the laser welding technology of the aluminum-silicon coated steel.
In the invention, the hot forming steel is ultra-high strength steel, and has excellent comprehensive mechanical properties, so that the hot forming steel is widely applied to manufacturing structural members such as a column A, a column B, front and rear bumpers of a car body and the like. The 22MnB5steel is a typical hot forming steel, which requires hot stamping and quenching during the production of the structural member to greatly improve the strength and hardness of the structural member. Because 22MnB5steel is easy to generate surface oxidation and decarburization during hot stamping, an aluminum-silicon coating is usually coated on the surface of the steel. In order to ensure excellent collision performance and safety performance of the structural member, steel plates with different strength levels or different thicknesses with equal strength levels are connected together in advance by using a laser welding technology, and then hot stamping is performed to obtain the structural member. The laser filler wire welding has the inherent advantages of laser welding, such as high energy density, small deformation, high welding efficiency and the like, can reduce the gap margin during butt welding, reduce welding defects and can regulate and control the weld seam tissue performance. Meanwhile, the plating layer removing treatment is not needed before welding, the direct welding of the aluminum-silicon plated steel strip plating layer can be realized, and the working procedure is simple.
Aiming at the problems existing in the welding of the aluminum-silicon coating steel, the currently used welding method is a patent applied by Ansalomide company, and the welding is performed after the aluminum-silicon coating is removed by laser ablation. According to the method, a plating layer ablation process is added in the production process of the splice welding plate, and the ablation speed is lower than the welding speed, so that the equipment investment cost is increased, the production efficiency is reduced, and the production cost is increased; more dust is generated in the cladding ablation process, centralized collection and treatment are needed, and meanwhile, the production auxiliary cost is increased. According to the patent of Ansalomide company (patent number: CN 101426612B), the tensile strength of the welded joint after the plating layer is removed is more than or equal to 1450MPa, and the level is similar to that of a base metal; when the filler wire is used for welding, the strength of the welded joint is greater than the level of a base metal due to the solid solution strengthening effect of alloy elements in the welding wire.
In recent literature, a process for welding aluminum-silicon coated steel using a pre-grooved variable energy distribution laser spot filler wire has been proposed (1]CovielloD,JanaVDH,RulloL,etal.Laserweldingoftailoredblanksmadeof Al-Si-coated22MnB5 steelmingafillrwirevariableengydistributionlasers [ J ].2023 ]), the present invention provides the following improvements over the prior art: firstly, the bevel angle in the comparison file is fixed by 9 degrees, which leads to difficult accurate control and complicated process in actual industrial production, and the invention does not need to be beveled in advance; secondly, the laser used for filler wire welding in the comparison document is not common laser, but special laser spots with variable energy distribution, the laser belongs to a semiconductor laser, the price of the laser is higher than that of an optical fiber laser, the requirement on the laser is more complex, new laser components are required to be customized, only the common optical fiber laser is required, and the price can be reduced by more than 1 time; thirdly, the beveled laser used in the comparison document is different from the laser used in the subsequent filler wire welding, so that the two lasers are needed, and only one laser is needed in the invention; fourth, the welding wire in the reference contains the noble alloying element molybdenum, which is not used in the present invention.
Compared with the prior art, the technical scheme of the invention has the following advantages:
compared with the prior art, the invention provides a method for manufacturing the splice welding plate with the aluminum-silicon coating. The aluminum-silicon coating hot forming steel is subjected to splice welding by utilizing the laser of the filling welding wire, the aluminum-silicon coating of the hot forming steel plate does not need to be removed before welding, the groove does not need to be formed before welding to reduce the entering amount of the coating, only a welding wire containing chromium and nickel with a certain proportion is adopted, and proper laser parameters are adjusted, so that alloy elements in the welding wire are melted in a high temperature and enter a welding pool, the original metallurgical reaction of liquid mixed metal is changed, an austenitic structure is formed, ferrite or brittle iron-aluminum intermetallic compound formation is restrained, the influence of aluminum elements on the austenitic structure is reduced, a martensitic structure is obtained, the mechanical property of a welding seam is improved, meanwhile, the production efficiency is greatly improved, and the cost is reduced.
Drawings
FIG. 1 is a graph showing the results of a stretching experiment.
Fig. 2 is a graph of mechanical properties of a welded joint.
FIG. 3 is a weld equilibrium phase diagram and quench phase diagram I.
FIG. 4 is a graph of tensile fracture testing of a weld after welding with filler wires of different chrome-nickel equivalent weights.
Fig. 5 is a weld equilibrium phase diagram and a quenching phase diagram ii.
Fig. 6 is a weld equilibrium phase diagram and a quench phase diagram iii.
Fig. 7 is a weld equilibrium phase diagram and a quench phase diagram iv.
Fig. 8 is a weld equilibrium phase diagram and quench phase diagram v.
Fig. 9 shows a weld equilibrium phase diagram and a quenching phase diagram vi.
Detailed Description
The present invention will be further described with reference to the accompanying drawings and specific examples, which are not intended to be limiting, so that those skilled in the art will better understand the invention and practice it.
In the following examples, filler wire chromium-nickel equivalent Cr eq /Ni eq According to Cr eq ＝1[Cr]+1.3[Si]+5.7[Al]+0.13[P]+0.08[S]，Ni eq ＝1[Ni]+31[C]+31[N]+0.6[Mn]The method comprises the steps of carrying out a first treatment on the surface of the Calculating; in [ Cr ]]、[Si]、[Al]、[P]、[S]、[Ni]、[C]、[N]And [ Mn ]]The mass fraction of each element in the filler wire.
Example 1
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.45wt% C,2wt% Cr,15wt% Ni,0.8wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 0.15;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Example 2
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.15wt% C,5wt% Cr,10wt% Ni,0.8wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 0.41;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Example 3
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.15wt% C,12wt% Cr,10wt% Ni,1.5wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 0.99;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Example 4
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.15wt% C,16wt% Cr,10wt% Ni,1.5wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 1.19;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Example 5
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.15wt% C,15wt% Cr,7.5wt% Ni,0.8wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 1.44;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Example 6
S1, taking two hot-formed steel plates with the same or different thickness and strength and aluminum-silicon coating, cleaning oil stains on the surfaces of the two hot-formed steel plates with the aluminum-silicon coating by using absolute ethyl alcohol, cooling and air-drying, and preparing a welding fixture for standby;
s2, butt-jointing the two heat-formed steel plates subjected to the purification treatment in the step S1 on a workbench and fixing the two heat-formed steel plates by using a welding fixture, wherein a gap exists between the two heat-formed steel plates;
s3, selecting a filler wire welding wire feeder, and setting the filler wire components and the machining parameters of a wire feeder; the wire feed speed was 2m/min.
The filler wire comprises 0.15wt% C,15wt% Cr,5wt% Ni,0.8wt% Mn;
chromium-nickel equivalent Cr of the filling welding wire eq /Ni eq Has a value of 1.79;
s4, selecting a laser, setting laser processing parameters, wherein the laser power is 4000W, the laser scanning speed is 3m/min, and the laser spot diameter is 0.03mm;
and S5, irradiating the welding wire in the step S3 and the butt joint position of the two hot-formed steel plates by adopting the laser in the step S4, and melting, solidifying and cooling the butt joint position and the welding wire to form a high-quality welding seam so as to finish the splicing of the two hot-formed steel plates.
Evaluation of Effect
As shown in FIG. 4, a-d are examples 1-4, e and f are examples 5 and 6, as comparative examples.
The welding experiment (welding power 500-6000W; welding speed 1-10m/min, wire feeding speed 1-10m/min, atmospheric environment welding, no preheating treatment and no groove) of the direct coating of the aluminum-silicon coating hot forming steel is carried out, and when the chromium-nickel equivalent Cr is adopted eq /Ni eq When the filler wire is welded in the range (less than or equal to 1.2), the tensile strength of the welding seam reaches the level of a base material (more than 1500 MPa), and the stretching fracture positions are all positioned on the base material (a-d in fig. 4); chromium-nickel equivalent Cr of filler wire eq /Ni eq Beyond the range of the present invention (greater than 1.2), the weld tensile fracture sites are located in the weld (e and f in FIG. 4).
It is apparent that the above examples are given by way of illustration only and are not limiting of the embodiments. Other variations and modifications of the present invention will be apparent to those of ordinary skill in the art in light of the foregoing description. It is not necessary here nor is it exhaustive of all embodiments. And obvious variations or modifications thereof are contemplated as falling within the scope of the present invention.
Claims (10)
1. The preparation method of the splice welding plate with the aluminum-silicon coating is characterized by comprising the following steps of:
s1: after purifying the hot-formed steel plates with the aluminum-silicon coating, placing the hot-formed steel plates at intervals to form gaps between the hot-formed steel plates with the aluminum-silicon coating;
s2: welding filler wires in the gaps by laser to obtain the splice welding plate with the aluminum-silicon coating; the filler wire comprises Fe, C, mn, cr, ni and a doping element, wherein the doping element is one or more of Si, al, P, S and N;
in the filler welding wire, [ C ] + [ Mn ] + [ Cr ] + [ Ni ] = 12-45%, wherein [ C ] < 0.5%, [ Mn ] < 3%, and [ Ni ] = 7.5-25%;
chromium-nickel equivalent Cr eq /Ni eq ≤1.2；
Wherein Cr is eq ＝1[Cr]+(1.3～1.8)[Si]+(5.3～5.8)[Al]+(0.10～0.15)[P]+(0.05～0.1)[S]，Ni eq ＝1[Ni]+(28～34)[C]+(27～31)[N]+(0.3～0.7)[Mn]The method comprises the steps of carrying out a first treatment on the surface of the In [ Cr ]]、[Si]、[Al]、[P]、[S]、[Ni]、[C]、[N]And [ Mn ]]Cr, si, al, P, S, ni, C, N and Mn, respectively, in the filler wire.
2. The method for producing a tailor welded blank with an aluminum-silicon coating according to claim 1, wherein the purification treatment is performed by degreasing the surface of the hot formed steel sheet with an aluminum-silicon coating with acetone or ethanol, cooling and air-drying.
3. The method of producing a tailor welded blank with an aluminum-silicon coating of claim 1, wherein the filler wire has a diameter greater than the width of the gap.
4. The method for manufacturing a splice welding plate with an aluminum-silicon coating according to claim 1, wherein in the step S2, the filler wire for laser welding is fed by a filler wire feeder.
5. The method for producing a tailor-welded blank with an aluminum-silicon coating according to claim 4, wherein the wire feeding speed is 1 to 10m/min.
6. The method for producing a tailor-welded blank with an al-si coating according to claim 1, wherein the total amount of C, mn, cr and Ni in the filler wire is 15 to 45% by mass fraction.
7. The method for producing a tailor-welded blank with an al-si coating according to claim 1, wherein the content of Cr in the filler wire is 2 to 12% by mass fraction.
8. The method for producing a tailor-welded blank with an al-si coating according to claim 1, wherein in the step S2, the power of the laser welding is 500-6000W, the scanning speed is 1-10m/min, and the laser spot diameter of the laser welding is 0.03-2.00 mm.
9. A tailor-welded blank with an aluminium-silicon coating produced by the production method of any one of claims 1 to 8.
10. A judging method for welding quality of a splice welding plate with an aluminum-silicon coating is characterized by comprising the following steps: detecting the components of Cr, si, al, P, S, ni, C, N and Mn in the welding wire during welding, and calculating the Cr-Ni equivalent Cr of the welding wire eq /Ni eq The method comprises the steps of carrying out a first treatment on the surface of the Wherein Cr is eq ＝1[Cr]+(1.3～1.8)[Si]+(5.3～5.8)[Al]+(0.10～0.15)[P]+(0.05～0.1)[S]，Ni eq ＝1[Ni]+(28～34)[C]+(27～31)[N]+(0.3～0.7)[Mn]，[Cr]、[Si]、[Al]、[P]、[S]、[Ni]、[C]、[N]And [ Mn ]]Cr, si, al, P, S, ni, C, N and Mn in the filler wire; if [ C ]]+[Mn]+[Cr]+[Ni]＝12～45％，[C]≤0.5％，[Mn]≤3％，[Ni]=7.5 to 25% and chromium-nickel equivalent Cr eq /Ni eq When the welding quality of the splice welding plate with the aluminum-silicon coating is less than or equal to 1.2, the welding quality of the splice welding plate with the aluminum-silicon coating is qualified; otherwise, the welding quality of the splice welding plate with the aluminum-silicon coating is unqualified.
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