CN114905149B - Laser powder filling welding and heat treatment method for coated steel - Google Patents

Laser powder filling welding and heat treatment method for coated steel Download PDF

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CN114905149B
CN114905149B CN202110171254.XA CN202110171254A CN114905149B CN 114905149 B CN114905149 B CN 114905149B CN 202110171254 A CN202110171254 A CN 202110171254A CN 114905149 B CN114905149 B CN 114905149B
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welding
coated steel
heat treatment
powder
laser
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CN114905149A (en
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许伟
杨上陆
陶武
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Shanghai Institute of Optics and Fine Mechanics of CAS
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Shanghai Institute of Optics and Fine Mechanics of CAS
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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
    • B23K26/00—Working by laser beam, e.g. welding, cutting or boring
    • B23K26/70—Auxiliary operations or equipment
    • 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
    • B23K26/70—Auxiliary operations or equipment
    • B23K26/702—Auxiliary equipment
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/25—Process efficiency

Abstract

The invention discloses a laser powder filling welding and heat treatment method of coated steel, which comprises the following steps: selecting manganese-chromium-nickel alloy powder which is uniformly mixed; clamping and fixing the two coated steel plates on a welding workbench; performing laser powder filling welding; and performing heat treatment after welding. By adding Mn-Cr-Ni alloy powder into the molten pool during welding, ferrite is inhibited from being generated, and the mechanical property of the welded joint is improved. The invention does not need to remove the coating before welding, can reduce the production cost and improve the production efficiency.

Description

Laser powder filling welding and heat treatment method for coated steel
Technical Field
The invention relates to a laser powder filling welding and heat treatment method of coated steel, which is used for welding coated steel and post-welding heat treatment, suppresses ferrite generation in welding seams, improves the mechanical properties of welding joints, and has good corrosion resistance and wear resistance.
Background
In order to reduce environmental pollution, strict automobile fuel efficiency and carbon dioxide emission standards are established all over the world. Developed countries of automobile industry such as European America are used for strengthening and improving own international competitiveness, continuously promoting and promoting the development of automobile energy saving technology, and aiming at improving the economic level of automobile fuel. This approach facilitates a series of new technologies and strategies for achieving weight savings in automobiles. The press-hardening steel (PHS) is one of the most important light-weight materials for realizing the light weight of the automobile and ensuring the safety of the automobile, can provide a full martensitic part with tensile strength higher than 1500MPa after hot stamping forming at 900-950 ℃, and is widely used for anti-collision structural members such as anti-collision beams, front and rear bumpers, A columns, B columns and the like of the automobile.
The aluminum-silicon coating has excellent oxidation resistance at high temperature, is generally applied to 22MnB5 boron steel by a hot dip method, but can also cause serious problems of reduced mechanical properties of welded joints. During laser welding, the coating may melt into the weld, softer ferrite may form in the fused region, and the ferrite may be larger in size near the fused boundary, severely degrading the mechanical properties of the welded joint. The current mainstream method applied in actual production is to remove the coating before welding and then match with a laser welding method, but the method has high cost and complex working procedure. Therefore, development of a high-efficiency and high-quality tailor-welding method for aluminum-silicon coated steel without removing the aluminum-silicon coating is needed, and the method has great significance for further application of the aluminum-silicon coated steel.
In CN 101426612B, a method for welding an aluminum-silicon coated steel to remove a coating is disclosed, and a steel wire brush or laser is used to remove the coating before welding, so that Al element in the coating is prevented from entering a welding line, and good welding quality is obtained. But this method increases the process steps and production costs before welding. Furthermore, oxidation and decarburization tend to occur in the uncoated region close to the weld during the austenitizing heat treatment. These uncoated areas are susceptible to corrosion when the component is put into service.
In CN 111975242A, a soldering paste and a process for improving the plasticity of a welding joint of a hot forming steel splice welding plate with an aluminum silicon coating are disclosed, and the soldering paste is coated on the welding surface of a plate, so that austenite grains and delta ferrite are refined, the uniformity of Al element is improved, and the welding quality is improved. However, the method is complex in operation, and the coated soldering paste also needs to be preheated at 350-500 ℃, so that the production process and cost are increased, and the production efficiency is reduced.
In CN 110900038A, a flux and process for laser welding of hot formed steel is disclosed, which improves the mechanical properties of the laser welded joint of the hot formed steel by removing or reducing the impact of the Al-Si coating on the weld quality by applying the flux. However, the method has complex process and low production efficiency, and the improved mechanical properties can not meet the requirements of actual production.
According to the laser welding method for the aluminum-silicon coating hot forming steel disclosed in CN 106475683B, metal nickel or metal chromium is filled in a gap between two steel plates before welding, and the metal nickel or metal chromium is melted into a welding line in the welding process, so that the formation of brittle Al-Fe metal compounds is inhibited, and the welding quality is improved. However, the method needs to pre-fill metallic nickel or metallic chromium in the splicing gap in advance, additionally increases the working procedure and cost before welding, and has low welding efficiency, thus being unfavorable for practical production.
Aiming at the limitations of complex process, high cost, substandard mechanical property and the like of the method, the laser welding method which does not need to remove a coating before welding and can improve the welding efficiency and the welding quality and ensure that the mechanical property meets the actual production requirement is necessary to be developed.
Disclosure of Invention
The invention provides a laser powder filling welding and heat treatment method of coated steel in view of the problems in the prior art, and aims to inhibit ferrite generation, ensure that a martensite microstructure with excellent mechanical properties is formed after quenching in a fusion zone, improve the mechanical properties of a welded joint, and have good corrosion resistance and wear resistance.
In order to achieve the above purpose, the technical scheme of the invention is as follows:
a laser powder filling welding and heat treatment method for coated steel comprises the following steps: selecting manganese-chromium-nickel alloy powder which is uniformly mixed; clamping and fixing the two coated steel plates on a welding workbench; performing laser powder filling welding; and performing heat treatment after welding.
Preferably, the manganese-chromium-nickel alloy powder comprises the following components in percentage by weight: 0.5-10%, cr:1-28%, ni:2-40%, the balance being iron and flux, said flux consisting of one or more of the following elemental powders: c is less than or equal to 10%, nb is less than or equal to 2%, si is less than or equal to 3%, mo is less than or equal to 10%, V is less than or equal to 2%, and the weight percentage of the flux in the manganese-chromium-nickel alloy powder is not more than 10%.
Preferably, the manganese-chromium-nickel alloy powder comprises the following components in percentage by weight: 1-7%, cr:5-25%, ni:5-35%, the balance being iron and flux, said flux consisting of one or more of the following elemental powders: c is less than or equal to 10%, nb is less than or equal to 2%, si is less than or equal to 3%, mo is less than or equal to 10%, V is less than or equal to 2%, and the weight percentage of the flux in the manganese-chromium-nickel alloy powder is not more than 10%.
Preferably, the powder feeding mode of the laser powder filling welding comprises the step of pre-filling powder on the welding surfaces of the two coated steel plates or in the clamping gaps of the two coated steel plates before welding, and the step of feeding powder by a paraxial or coaxial mode is adopted in the welding process.
Preferably, a laser beam is used for welding the two coated steel plates in the welding process, and manganese-chromium-nickel alloy powder enters a molten pool; and cooling and solidifying the molten pool to form a welding line.
Preferably, the welding surface of the coated steel plates or the clamping gap between the two coated steel plates is pre-filled with powder, the welding process adopts paraxial powder feeding or coaxial powder feeding, the maximum splicing gap is not more than 20% of the plate thickness, the filling quantity of the manganese-chromium-nickel alloy powder is calculated by the sectional area of a vertical welding line, and the ratio of the area of the filling quantity to the sectional area of the welding line is lower than 50%; the residual height of the weld joint formed by the filling manganese-chromium-nickel alloy powder is less than 25% of the plate thickness.
Preferably, the coating is produced by interdiffusion between the steel plate substrate and the coating of aluminum and aluminum alloys; the base materials of the areas to be welded of the two steel plates are at least provided with one coating; the total thickness of the coating is less than 65 mu m; the thickness of the coated steel plate is 0.2-4mm.
Preferably, the heat treatment means heating the two joined steel plates, transferring after the heating and heat preservation are finished, and quenching by adopting a forming die with a water cooling system or water cooling quenching.
Preferably, the heating temperature of the heat treatment is 830-1050 ℃, the heat preservation time is 1-60 min, and the cooling speed is more than or equal to 27 ℃/s.
Preferably, the laser includes a fiber laser, a solid state laser, a semiconductor laser, a gas laser.
Preferably, the walking track of the laser beam comprises a non-swinging mode and a swinging mode.
Preferably, the welding process can be performed directly in air using a non-shielding gas.
Preferably, the laser beam comprises one or a combination of multiple beams.
The invention has the following advantages over the existing coating welding method.
1) The coating is not required to be removed before welding, so that the cost can be reduced and the welding efficiency can be improved.
2) The defects of low absorptivity of the material to laser and high welding energy consumption are effectively overcome.
3) Can obviously inhibit ferrite from being generated and improve the mechanical property of the welded joint.
4) The welded joint has excellent wear resistance and corrosion resistance.
Drawings
Features and advantages of the examples of the present disclosure will become apparent to those skilled in the art from the following detailed description and drawings, wherein the drawings are merely some embodiments of the invention and from which other drawings may be derived without inventive work.
FIG. 1 shows a schematic diagram of a powder laser welding method performed in a clamping gap of a steel plate;
FIG. 2 shows a schematic view of a powder laser welding method performed on a welding surface of a steel plate;
FIG. 3 shows a schematic diagram of a paraxial powder feed laser welding method;
FIG. 4 shows a schematic diagram of a coaxial powder feed laser welding method;
FIG. 5 shows a schematic diagram of the fill volume versus cross-sectional area of a weld;
FIG. 6 shows an SEM image of the microstructure of a weld of the present invention;
FIG. 7 shows a temperature-phase organization result graph of the present invention;
FIG. 8 shows an SEM image of the microstructure of a laser self-welding weld;
fig. 9 shows a graph of temperature-phase structure results of laser self-welding.
Detailed Description
In order that the above objects, technical solutions and advantages of the present invention may be more readily understood, embodiments of the present invention will now be described in detail with reference to the accompanying drawings. It should be understood that the present invention is not limited to the following embodiments and is embodied in various forms, and those skilled in the art should understand the present invention from the spirit of the following embodiments. The scope of the invention is limited only by the claims.
Due to the presence of the aluminum-silicon coating, the coating melts into a molten pool during laser welding, resulting in an increase in the content of Al element in the molten pool. After heat treatment, the weld joint structure is a mixed structure of ferrite and martensite with higher content, so that the mechanical property of the welded joint is greatly reduced.
Therefore, how to inhibit ferrite generation in the welding line is a key for improving the mechanical property of the aluminum-silicon coating laser welding joint. Based on the thought of inhibiting ferrite generation, the invention can inhibit ferrite generation by adding Mn-Cr-Ni alloy powder into a molten pool in the laser welding process, so as to achieve the aim of improving the mechanical property of a welded joint.
The roles of the elements of the present invention are as follows.
C: the carbon element stabilizes the austenite phase, lowering the Ac3 temperature and thus lowering the thermoforming temperature. Carbon is a interstitial solid solution element, and its strengthening effect is much greater than that of a substitutional solid solution element. With the increase of the carbon content in the steel, the carbon content in the martensite after quenching also increases, thereby improving the strength of the martensite. Therefore, strength can be improved by increasing the carbon content under the condition that hardenability is ensured. However, as the carbon content increases, the toughness of the steel sheet decreases, the weldability deteriorates, and the carbon content is generally not excessively high.
Mn: manganese can improve hardenability, is also a stabilizing element of austenite, reduces Ac3 temperature, and is beneficial to reducing hot stamping temperature so as to refine prior austenite grains. Mn and O, S have stronger binding force, are good deoxidizing agents and desulfurizing agents, can weaken or eliminate the hot brittleness of steel caused by sulfur, and improve the hot workability of the steel. Too high a Mn content may reduce the oxidation resistance of the steel while deteriorating welding and formability.
Ni: the nickel element can not only enlarge the austenite phase region, but also improve the hardenability of the steel. The nickel element with proper amount can promote austenite transformation, inhibit ferrite generation and improve welding quality. The nickel element is too little and the effect is not obvious. Too high nickel content can result in increased retained austenite in the weld joint and can also increase production costs.
Cr: the main function of chromium element can improve corrosion resistance. Chromium is also a strong carbide forming element, is extremely easy to form carbide with carbon element, and can effectively inhibit the growth of crystal grains. The appropriate amount of chromium can increase the corrosion resistance of the welding seam, and the chromium also acts together with nickel element to ensure that the welding seam obtains a full martensitic structure and improves the mechanical property of the welding joint. When the chromium element is too low, the corrosion resistance is lowered. When the chromium element is too high, the weld joint can form higher ferrite, and the mechanical property of the welded joint is reduced.
Si: silicon is an effective deoxidizer, has a strong solid solution strengthening effect, can inhibit cementite precipitation in the tempering process, and improves the tempering stability of steel, but the excessive silicon content can cause surface quality problems.
Mo, nb, V: molybdenum can obviously improve the hardenability of steel, can effectively inhibit ferrite from generating, and can also improve the weldability and corrosion resistance of steel. Molybdenum, niobium and vanadium are carbide forming elements, so that grains can be refined, and the strength and toughness of the steel can be improved.
It should be noted that C, si, mo, nb, V is not an essential element for the method of the present invention.
Example 1
Fig. 1 depicts a laser powder filling welding method of the first embodiment, wherein the thickness of each of the coated steel plate 4 and the coated steel plate 5 is 1.4mm, and the upper and lower surfaces of each of the coated steel plate 4 and the coated steel plate 5 are provided with an aluminum silicon coating 7, wherein the coating 7 comprises an aluminum silicon layer and an aluminum iron alloy layer. Two coated steel plates 4 and 5 were fixed on a welding table using a jig, and a gap of 0.2mm was set. The gap is filled with manganese-chromium-nickel alloy powder 3 prior to laser tailor welding. And welding a region to be welded by using a laser beam 1, fusing molten metal of the two aluminum-silicon coated steel plates with manganese-chromium-nickel alloy powder 3, and cooling to form a welding seam 6. Wherein the proportion of the manganese chromium nickel alloy powder 3 is as follows: mn:4%, cr:10%, ni:20%, the balance being Fe and flux. After laser welding, placing the welding plate in a heating furnace at 950 ℃, heating and preserving heat for 5min, and transferring the welding plate for quenching. The metallographic structure of the welding seam is detected, and the result shows that the microstructure of the welding seam is full martensite.
Example 2
Fig. 2 depicts a laser powder filling welding method of a second embodiment, wherein the thickness of each of the coated steel plate 4 and the coated steel plate 5 is 1.5mm, and the upper and lower surfaces of each of the coated steel plate 4 and the coated steel plate 5 are provided with an aluminum-silicon coating 7, wherein the coating 7 comprises an aluminum-silicon layer and an aluminum-iron alloy layer. The two coated steel plates 4 and 5 were fixed on a welding table using a jig, and the splice welding gap of the two coated steel plates was zero. And filling the surface of the area to be welded with Mn-Cr-Ni alloy powder 3 before laser tailor-welding. And welding a region to be welded by using a laser beam 1, fusing molten metal of the two aluminum-silicon coated steel plates with manganese-chromium-nickel alloy powder 3, and cooling to form a welding seam 6. Wherein the proportion of the manganese chromium nickel alloy powder 3 is as follows: mn:1.5%, cr:18%, ni:30%, the balance being Fe and flux. After laser welding, placing the welding plate in a heating furnace at 950 ℃, heating and preserving heat for 5min, and transferring the welding plate for quenching. The metallographic structure of the welding seam is detected, and the result shows that the microstructure of the welding seam is full martensite.
Example 3
Fig. 4 depicts a laser powder filling welding method of a third embodiment, wherein the thickness of each of the coated steel plate 4 and the coated steel plate 5 is 1.4mm, and the upper and lower surfaces of each of the coated steel plate 4 and the coated steel plate 5 are provided with an aluminum-silicon coating 7, wherein the coating 7 comprises an aluminum-silicon layer and an aluminum-iron alloy layer. The two coated steel plates 4 and 5 were fixed on a welding table using a jig, and the splice welding gap of the two coated steel plates was zero. In the laser welding process, the coaxial powder feeding device 9 feeds powder into a molten pool, molten metal of two aluminum-silicon coated steel plates is fused with the manganese-chromium-nickel alloy powder 3, and the molten metal is cooled to form a welding seam 6. Wherein the proportion of the manganese chromium nickel alloy powder 3 is as follows: mn:3%, cr:23%, ni:15%, the balance being Fe and flux. After laser welding, placing the welding plate in a heating furnace at 950 ℃, heating and preserving heat for 5min, and transferring the welding plate for quenching. The metallographic structure of the welding seam is detected, and the result shows that the microstructure of the welding seam is full martensite. In another embodiment, the coaxial powder feeding mode can be changed into the paraxial powder feeding mode, as shown in fig. 3.
Fig. 5 shows a schematic cross-sectional view of a vertical weld after heat treatment of a laser welded joint filled with manganese-chromium-nickel alloy powder. The area 11 of the welding seam cross section is the welding seam area S of an area parallel to the minimum height of the upper surface and the lower surface of the two steel plates 0 The method comprises the steps of carrying out a first treatment on the surface of the The area 14 of the welding seam cross section is the welding seam area S higher than the minimum height area of the two steel plates 1 The method comprises the steps of carrying out a first treatment on the surface of the The area 15 of the welding seam cross section is lower than the welding seam area S of the bottom surface areas of the two plates 2 The area 10 of the welding seam cross section is the cross section S of the gap between two steel plates 3 The method comprises the steps of carrying out a first treatment on the surface of the 12 is the length of the upper excess of the weld; 13 is the length of the remaining height of the weld. Ratio k= (S) of cross-sectional area of filling amount to cross-sectional area of weld 1 +S 2 +S 3 )/(S 0 +S 1 +S 2 ) Wherein K is less than 50%.
FIG. 6 shows a typical weld microstructure of the above inventive examples, the microstructure being fully martensitic and temperature-structural phase analysis of the elemental content of the weld, as shown in FIG. 7. The result shows that the manganese-chromium-nickel alloy powder is filled in the welding process, so that ferrite can be obviously inhibited from being generated, and the microstructure of the full martensite can be obtained.
Comparative example 1
The laser self-fluxing welding is adopted to splice-weld the 1.4mm aluminum-silicon coated steel plate, the butt joint gap is zero, and the manganese-chromium-nickel alloy powder is not filled. After the welding, the metallographic structure of the welding seam is detected after the heat treatment, and the microstructure of the welding seam is a ferrite and martensite mixed structure, as shown in fig. 8. Temperature-phase analysis was performed based on the elemental content of the weld structure of laser self-fluxing welding, as shown in FIG. 9. The results show that when higher aluminum elements are present in the weld, more ferrite is produced.
In summary, the invention can obtain a microstructure of full martensite by adding the manganese-chromium-nickel alloy powder to the molten pool during welding without removing the coating, thereby suppressing the generation of ferrite. Not only can improve welding quality and production efficiency, but also can reduce cost.
The above examples of the method according to the invention are intended to illustrate the invention by way of example and not to limit the invention. It should be apparent to those skilled in the art that any possible variations or substitutions may be made without departing from the spirit of the invention and are within the scope of the invention.

Claims (8)

1. A laser powder filling welding and heat treatment method for coated steel is characterized in that: selecting manganese-chromium-nickel alloy powder which is uniformly mixed; clamping and fixing the two coated steel plates on a welding workbench; performing laser powder filling welding; performing heat treatment after welding;
the manganese-chromium-nickel alloy powder comprises the following components in percentage by weight: 0.5-10%, cr:1-28%, ni:2-40%, the balance being iron and flux, said flux consisting of one or more of the following elemental powders: c is less than or equal to 10%, nb is less than or equal to 2%, si is less than or equal to 3%, mo is less than or equal to 10%, V is less than or equal to 2%, and the weight percentage of the flux is not more than 10% of the manganese-chromium-nickel alloy powder;
the filling amount of the manganese-chromium-nickel alloy powder is calculated by the sectional area of the vertical welding seam, and the ratio of the area of the filling amount to the sectional area of the welding seam is lower than 50%; the residual height of the weld joint formed by filling the manganese-chromium-nickel alloy powder is less than 25% of the plate thickness.
2. The laser powder filling welding and heat treatment method for coated steel according to claim 1, wherein: the manganese-chromium-nickel alloy powder comprises the following components in percentage by weight: 1-7%, cr:5-25%, ni:5-35%, the balance being iron and flux, said flux consisting of one or more of the following elemental powders: c is less than or equal to 10%, nb is less than or equal to 2%, si is less than or equal to 3%, mo is less than or equal to 10%, V is less than or equal to 2%, and the weight percentage of the flux in the manganese-chromium-nickel alloy powder is not more than 10%.
3. The laser powder filling welding and heat treatment method for coated steel according to claim 1, wherein: the powder feeding mode of laser powder filling welding comprises the step of pre-filling powder on the welding surfaces of the two coated steel plates or in the clamping gaps of the two coated steel plates before welding, and the step of adopting a paraxial powder feeding or a coaxial powder feeding in the welding process.
4. The laser powder filling welding and heat treatment method for coated steel according to claim 1, wherein: welding the two coated steel plates by using a laser beam in the welding process, wherein the manganese-chromium-nickel alloy powder enters a molten pool; and cooling and solidifying the molten pool to form a welding line.
5. The laser powder filling welding and heat treatment method for coated steel according to claim 1, wherein: and (3) pre-filling powder on the welding surface of the coated steel plate or in the clamping gap of the two coated steel plates, wherein the welding process adopts paraxial powder feeding or coaxial powder feeding, and the maximum splicing gap is not more than 20% of the plate thickness.
6. The laser powder filling welding and heat treatment method of coated steel according to any one of claims 1-5, said coating resulting from interdiffusion between the steel plate substrate and the coating of aluminum and aluminum alloys; the base materials of the areas to be welded of the two steel plates are at least provided with one coating; the total thickness of the coating is less than 65 mu m; the thickness of the coated steel plate is 0.2-4mm.
7. The laser powder filling welding and heat treatment method for coated steel according to claim 1, wherein: the heat treatment is to heat the two joined steel plates, transfer the steel plates after the heating and heat preservation are finished, and cool the steel plates with water.
8. The laser powder filling welding and heat treatment method for coated steel according to claim 7, wherein: the heating temperature of the heat treatment is 830-1050 ℃, the heat preservation time is 1-60 min, and the cooling speed is more than or equal to 27 ℃/s.
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