CN112894113A - Aluminum-magnesium heterogeneous alloy post-welding treatment process and application thereof - Google Patents
Aluminum-magnesium heterogeneous alloy post-welding treatment process and application thereof Download PDFInfo
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- 238000003466 welding Methods 0.000 title claims abstract description 87
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 59
- 239000000956 alloy Substances 0.000 title claims abstract description 59
- 238000000034 method Methods 0.000 title claims abstract description 50
- 230000008569 process Effects 0.000 title claims abstract description 43
- SNAAJJQQZSMGQD-UHFFFAOYSA-N aluminum magnesium Chemical compound [Mg].[Al] SNAAJJQQZSMGQD-UHFFFAOYSA-N 0.000 title claims abstract description 34
- 238000000462 isostatic pressing Methods 0.000 claims abstract description 18
- 230000035939 shock Effects 0.000 claims abstract description 10
- 238000002635 electroconvulsive therapy Methods 0.000 claims abstract description 7
- 238000004021 metal welding Methods 0.000 claims abstract description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 22
- 230000003068 static effect Effects 0.000 claims description 13
- 238000001816 cooling Methods 0.000 claims description 11
- 229910052757 nitrogen Inorganic materials 0.000 claims description 11
- 239000011261 inert gas Substances 0.000 claims description 10
- 239000007789 gas Substances 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 4
- 230000009467 reduction Effects 0.000 claims description 4
- 239000007787 solid Substances 0.000 claims description 4
- 239000006104 solid solution Substances 0.000 claims description 4
- 238000005086 pumping Methods 0.000 claims description 3
- 238000004381 surface treatment Methods 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 2
- 239000001307 helium Substances 0.000 claims description 2
- 229910052734 helium Inorganic materials 0.000 claims description 2
- SWQJXJOGLNCZEY-UHFFFAOYSA-N helium atom Chemical compound [He] SWQJXJOGLNCZEY-UHFFFAOYSA-N 0.000 claims description 2
- 239000007788 liquid Substances 0.000 claims description 2
- 229910000861 Mg alloy Inorganic materials 0.000 abstract description 16
- 229910000838 Al alloy Inorganic materials 0.000 abstract description 15
- 230000007547 defect Effects 0.000 abstract description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 9
- 239000013078 crystal Substances 0.000 abstract description 5
- 239000011777 magnesium Substances 0.000 abstract description 5
- 238000009826 distribution Methods 0.000 abstract description 4
- 239000011148 porous material Substances 0.000 abstract description 3
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 abstract description 2
- 238000005728 strengthening Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 238000012360 testing method Methods 0.000 description 8
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 230000035882 stress Effects 0.000 description 6
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- 238000005299 abrasion Methods 0.000 description 4
- 239000011888 foil Substances 0.000 description 4
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 3
- 239000001257 hydrogen Substances 0.000 description 3
- 229910052739 hydrogen Inorganic materials 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 238000007711 solidification Methods 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- 239000002344 surface layer Substances 0.000 description 3
- 230000008646 thermal stress Effects 0.000 description 3
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 229910021323 Mg17Al12 Inorganic materials 0.000 description 2
- 238000004140 cleaning Methods 0.000 description 2
- 239000011248 coating agent Substances 0.000 description 2
- 238000000576 coating method Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000003912 environmental pollution Methods 0.000 description 2
- 239000004519 grease Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910001234 light alloy Inorganic materials 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005457 optimization Methods 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
- 230000000704 physical effect Effects 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 229910000679 solder Inorganic materials 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Classifications
-
- 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
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/02—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating by means of a press ; Diffusion bonding
- B23K20/021—Isostatic pressure 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
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/24—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
- B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
- B23K20/26—Auxiliary equipment
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- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Laser Beam Processing (AREA)
- Pressure Welding/Diffusion-Bonding (AREA)
Abstract
The invention relates to the field of non-ferrous metal welding, in particular to an aluminum-magnesium heterogeneous alloy post-welding treatment process and application thereof. The process firstly carries out laser shock treatment on the aluminum-magnesium heterogeneous alloy welded joint to strengthen the surface tissue form of the welded joint, improves the surface quality, then carries out warm isostatic pressing treatment to close the tissue defects of pores, shrinkage porosity and the like in the microstructure in the welded joint, breaks the net distribution of beta-Mg 17Al12 precipitated phases at the crystal boundary, obviously improves the quality of the cast structure of the welded joint, and finally carries out ultralow temperature treatment to effectively eliminate the welding residual stress. In addition, the process is simple in implementation scheme, can adjust the process parameters of laser shock, warm isostatic pressing and ultralow temperature treatment according to different welding joint types, and has important significance for expanding the engineering application of the aluminum and magnesium alloy.
Description
Technical Field
The invention relates to the field of non-ferrous metal welding, in particular to an aluminum-magnesium heterogeneous alloy post-welding treatment process and application thereof.
Background
The information in this background section is only for enhancement of understanding of the general background of the invention and is not necessarily to be construed as an admission or any form of suggestion that this information forms the prior art that is already known to a person of ordinary skill in the art.
Energy shortage and environmental pollution are outstanding problems in the world at present, and reducing the weight of the automobile and the aeronautics and astronautics become effective methods for reducing the environmental pollution and saving energy in the fields of automobiles, aerospace and the like. According to statistics, the oil consumption can be reduced by 0.7 liter when the automobile mass is reduced by 100 kilograms. In aerospace vehicles, the reduction in weight of structural components leads to a reduction in fuel costs which is 100 times that of the automotive industry. Aluminum alloy and magnesium alloy are the lightest metal structure materials at present, have the advantages of small density, high specific strength, easy forming and the like, and are widely applied in the fields of aerospace, automotive electronics and the like. In the automobile field, the aluminum alloy and the magnesium alloy can be used as key parts such as an engine, an automobile chassis and the like besides being used as an instrument panel base, a seat frame, a steering wheel shaft, a gearbox shell and the like, and have wide application prospects in the automobile field.
Aluminium alloyThe welding of the heterogeneous alloy with the magnesium alloy is an indispensable important part in the engineering application process, and how to effectively improve the service reliability of the aluminum-magnesium heterogeneous alloy welding joint is one of the key technical problems which are urgently needed to be solved in the field of aluminum and magnesium light alloys at present. Limited by the physical and chemical properties of the aluminum alloy and the magnesium alloy, the aluminum-magnesium heterogeneous alloy has high welding difficulty and relatively low mechanical property of a welding joint. Such as: (1) in the welding process of the aluminum alloy and the magnesium alloy, the air entrainment is easy to occur, the entrained nitrogen bubbles and hydrogen bubbles are low in buoyancy, and because the cooling speed of the molten metal in the welding seam area is high, a large amount of hydrogen and nitrogen are difficult to escape, and finally the hydrogen and nitrogen remain in the welding seam in the form of air holes which become crack expansion sources in the service process of the welding joint; (2) the welding pool of the aluminum alloy and the magnesium alloy can cause micro defects such as shrinkage cavity, looseness and the like due to volume shrinkage in the solidification process, and also has adverse effect on the service performance of a welding joint; (3) the thermal expansion coefficient of the aluminum alloy and the magnesium alloy is about 2 times that of the steel material, and the expansion during heating and the shrinkage deformation during solidification and cooling are very obvious in the welding process, so that large residual thermal stress exists after welding, and the mechanical property of a welding joint is seriously influenced; (4) when aluminum alloy and magnesium alloy are subjected to dissimilar alloy welding, beta-Mg is formed inside a welded joint due to nonequilibrium solidification17Al12And the precipitated phase is distributed in a net shape at the crystal boundary, so that the mechanical property of the aluminum-magnesium heterogeneous alloy welding joint is greatly damaged.
The problems of air holes and residual stress of the welding joint of the aluminum alloy and the magnesium alloy are very prominent due to the limitation of the physical properties of the aluminum alloy and the magnesium alloy. From the viewpoints of ensuring the integrity of a welding structure, the rationality of a manufacturing process, the reliability of a using process and the like, the deformation, the fracture, the failure and the like of an engineering assembly caused by welding problems such as air hole defects, hard and brittle reticular precipitated phases, residual stress and the like seriously limit the engineering application of aluminum-magnesium heterogeneous alloy welding pieces. Therefore, how to effectively eliminate welding structure defects such as welding pores and the like, greatly reduce welding residual stress, powerfully enhance the quality of a welding joint of the aluminum-magnesium heterogeneous alloy, and improve the service performance of the aluminum-magnesium heterogeneous alloy becomes one of bottleneck technologies and key technologies to be solved urgently, which restrict the engineering application of aluminum alloys and magnesium alloys.
Disclosure of Invention
In order to solve the defects of the prior art, the invention provides an aluminum-magnesium heterogeneous alloy post-welding treatment process. The process firstly carries out laser shock treatment on the aluminum-magnesium heterogeneous alloy welded joint to strengthen the surface tissue form of the welded joint, improves the surface quality, then carries out warm isostatic pressing treatment to close the tissue defects of pores, shrinkage porosity and the like in the microstructure in the welded joint, breaks the net distribution of beta-Mg 17Al12 precipitated phases at the crystal boundary, obviously improves the quality of the cast structure of the welded joint, and finally carries out ultralow temperature treatment to effectively eliminate the welding residual stress.
In order to achieve the technical purpose, the first aspect of the invention provides an aluminum-magnesium heterogeneous alloy post-welding treatment process, which specifically comprises the following steps:
(1) carrying out surface treatment on the aluminum-magnesium heterogeneous alloy welding piece to remove oil stains and dirt;
(2) carrying out surface laser shock treatment on the aluminum-magnesium heterogeneous alloy welding piece with the treated surface;
(3) putting an aluminum-magnesium heterogeneous alloy welding piece into a warm isostatic pressing device, fixing by using a fixture, introducing inert gas for gas pressurization heat treatment, recovering the welding piece to room temperature along with a furnace after the treatment process is finished, releasing the inert gas, reducing the static pressure of a cavity, unloading the welding piece after the temperature is recovered to the room temperature, and taking out the welding piece;
(4) and after the warm isostatic pressing treatment is finished, gradually cooling the environment temperature of the cavity to ultralow temperature for ultralow temperature treatment, slowly recovering to room temperature after the ultralow temperature treatment is finished, and taking out the aluminum-magnesium heterogeneous alloy welding piece.
The invention provides an application of an aluminum-magnesium heterogeneous alloy postweld treatment process in the field of metal welding.
One or more embodiments of the present invention have at least the following advantageous effects:
(1) according to the invention, the combined post-welding process optimization of laser shock strengthening, warm isostatic pressing treatment and ultralow temperature treatment is carried out on the aluminum alloy or magnesium alloy welding joint, so that the microstructure of an aluminum-magnesium welding part is obviously improved, and the mechanical property is greatly improved.
The surface layer of the welded joint is subjected to severe plastic deformation by laser shock strengthening and ultra-high pressure generated by laser within nanosecond time, so that high-density dislocation tangle and a surface layer superfine crystal structure are formed, and the purpose of greatly strengthening the strength, hardness and corrosion resistance of the surface layer of the welded joint is achieved.
Through warm isostatic pressing treatment, plastic flow diffusion occurs inside the welded joint, micro-structure holes are bonded and closed, the welded joint is more uniform and compact in structure, and the occupied space of defects such as air holes and shrinkage porosity is macroscopically limited, so that the size or the shape of the welded joint cannot be changed. In addition, by warm isostatic pressing, β -Mg is broken up17Al12The network structure of precipitated phase at the grain boundary changes beta-Mg17Al12The distribution form of the precipitated phase obviously improves the performance of the aluminum-magnesium heterogeneous alloy welding joint.
Based on a thermal elastic-plastic mechanical model of the material, the residual stress of the welded joint is further eliminated through cryogenic treatment, and the precipitation of a microscopic metastable state phase can be promoted through ultralow temperature treatment, so that the dislocation density is improved, the capability of crystal grains for resisting microscopic plastic deformation is improved, and the wear resistance and the dimensional stability of the welded part are greatly improved.
(2) The method has simple implementation scheme, can adjust the process parameters of laser shock, temperature isostatic pressing and ultralow temperature treatment according to different welding joint types, effectively eliminates the welding residual thermal stress, eliminates the defects of microstructure air holes and the like of the welding joint, and breaks through beta-Mg17Al12The network distribution of the precipitated phase improves the surface quality, greatly improves the microstructure and the mechanical property of the aluminum-magnesium heterogeneous alloy welding joint, and has important significance for expanding the engineering application of the aluminum and magnesium alloy.
Detailed Description
It is to be understood that the following detailed description is exemplary and is intended to provide further explanation of the invention as claimed. Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs.
It is noted that the terminology used herein is for the purpose of describing particular embodiments only and is not intended to be limiting of exemplary embodiments according to the invention. As used herein, the singular forms "a", "an" and "the" are intended to include the plural forms as well, and it should be understood that when the terms "comprises" and/or "comprising" are used in this specification, they specify the presence of stated features, steps, operations, devices, components, and/or combinations thereof, unless the context clearly indicates otherwise.
As introduced in the background art, gas is easily involved in the welding process of the aluminum and magnesium alloys to form air holes, the thermal expansion coefficient is large, and large welding thermal residual stress exists after welding, so that the service performance of an aluminum alloy and magnesium alloy welding joint is poor in the engineering application process, and in order to solve the technical problems, the invention provides an aluminum-magnesium heterogeneous alloy post-welding treatment process which specifically comprises the following steps:
(1) carrying out surface treatment on the aluminum-magnesium heterogeneous alloy welding piece to remove oil stains and dirt;
(2) carrying out surface laser shock treatment on the aluminum-magnesium heterogeneous alloy welding piece with the treated surface;
(3) putting an aluminum-magnesium heterogeneous alloy welding piece into a warm isostatic pressing device, fixing by using a fixture, introducing inert gas for gas pressurization heat treatment, recovering the welding piece to room temperature along with a furnace after the treatment process is finished, releasing the inert gas, reducing the static pressure of a cavity, unloading the welding piece after the temperature is recovered to the room temperature, and taking out the welding piece;
(4) and after the warm isostatic pressing treatment is finished, gradually cooling the environment temperature of the cavity to ultralow temperature for ultralow temperature treatment, slowly recovering to room temperature after the ultralow temperature treatment is finished, and taking out the aluminum-magnesium heterogeneous alloy welding piece.
In one or more embodiments of the invention, in the step (2), a Nd-YAG solid laser is adopted for laser shock, the energy of the laser is 2.5-7J, the wavelength is 1.064 μm, the frequency is 0.4-1 Hz, and the diameter of a light spot is 2.5-6 mm;
wherein, the laser impact time is determined according to the size of the processing style and the moving speed of the laser head.
In one or more embodiments of the present invention, in the step (3), the inert gas is helium, argon, or nitrogen;
in one or more embodiments of the present invention, in step (3), before the inert gas is introduced, the vacuum degree is first reduced to below 15 mPa;
in one or more embodiments of the invention, in the step (3), in the process of filling nitrogen into the cavity, the static gas pressure is controlled to be about 60MPa, and after the treatment temperature required by the welding joint is stable, the static gas pressure is adjusted to be 100-200 MPa;
in one or more embodiments of the invention, in the step (3), the warm isostatic pressing treatment time is 3-4h, the temperature is determined according to the solid solution temperature of different alloys, and the temperature below the solid solution temperature is selected to be 10-15 ℃ as the corresponding treatment temperature.
In one or more embodiments of the present invention, in the step (4), the temperature of the cavity is controlled by pumping liquid nitrogen, so that the temperature of the cavity can be adjusted within a range from room temperature to-190 ℃;
in one or more embodiments of the invention, in the step (4), the temperature control precision is +/-1 ℃, the temperature reduction rate is controlled to be 10-20 ℃/min, the ultralow temperature treatment temperature is-130 to-180 ℃, and the treatment time is 5-7 h;
the invention provides an application of an aluminum-magnesium heterogeneous alloy postweld treatment process in the field of metal welding.
In order to make the technical solution of the present invention more clearly understood by those skilled in the art, the technical solution of the present invention will be described in detail below with reference to specific examples and comparative examples.
Example 1
And (3) performing multi-process combined post-weld strengthening treatment on the 5052-AZ31 heterogeneous alloy welding joint:
(1) the thickness of the 5052-AZ31 hetero-alloy welding joint plate is 4mm, the size of the welding joint plate is 110 multiplied by 130mm, surface dirt is removed by a steel brush before treatment, and surface grease is removed by acetone;
(2) selecting an Nd YAG solid laser with the wavelength of 1.064 mu m, the frequency of 0.5Hz and the spot diameter of 3mm, coating aluminum foil on the surface of a 5052-AZ31 heterogeneous alloy welding joint, and performing surface laser shock strengthening treatment;
(3) after laser shock treatment, removing aluminum foil on the surface of the sample, and cleaning the surface by using alcohol;
(4) putting the 5052-AZ31 heterogeneous alloy welding joint into a warm isostatic pressing device, pumping the vacuum degree to be below 15mPa, introducing nitrogen, controlling the static gas pressure to be about 60MPa, and continuously increasing the temperature of a cavity to 250 ℃ at the heating rate of 50 ℃/h; (ii) a
(5) After the temperature is stabilized, the static air pressure is increased to 135MPa and is kept stable;
(6) the 5052-AZ31 heterogeneous alloy welding joint is processed for 3.5 hours in the environment of the cavity temperature of 250 ℃ and the static air pressure of 135 MPa;
(7) after the treatment is finished, taking out the 5052-AZ31 heterogeneous alloy welding joint after the processes of cooling, decompressing and unloading;
(8) placing the 5052-AZ31 heterogeneous alloy welding joint into a low-temperature environment box, controlling the cooling rate at 15 ℃/min, finally cooling to-150 ℃, treating for 5h, and recovering to the room temperature at the heating rate of 20 ℃/min after the treatment is finished;
(8) after the treatment is finished, the 5052-AZ31 heterogeneous alloy welded joint is taken out, the tensile property is tested, the tensile strength reaches 89.3MPa, and the test results are shown in table 1.
Example 2
Carrying out multi-process combined post-weld strengthening treatment on the 5754-AZ80 heterogeneous alloy welding joint:
(1) the thickness of the 5754-AZ80 hetero-alloy welding joint plate is 3mm, the size is 115 multiplied by 140mm, surface dirt is removed by a steel brush before treatment, and surface grease is removed by acetone;
(2) selecting an Nd YAG solid laser with the wavelength of 1.064 mu m, the frequency of 0.6Hz and the spot diameter of 4mm, coating aluminum foil on the surface of a 5754-AZ80 heterogeneous alloy welding joint, and performing surface laser shock strengthening treatment;
(3) after laser shock treatment, removing aluminum foil on the surface of the sample, and cleaning the surface by using alcohol;
(4) placing the 5754-AZ80 heterogeneous alloy welding joint into a warm isostatic pressing device, introducing nitrogen, controlling the static pressure to be about 65MPa, and continuously increasing the temperature of the cavity to 270 ℃ at the temperature increase rate of 45 ℃/h; (ii) a
(5) After the temperature is stable, the static pressure is increased to 150MPa and kept stable;
(6)5754-AZ80 the welding joint of the heterogeneous alloy is processed for 4h in the environment of cavity temperature of 270 ℃ and static air pressure of 150 MPa;
(7) after the treatment is finished, taking out the 5754-AZ80 heterogeneous alloy welding joint after the processes of cooling, decompressing and unloading;
(8) putting the 5754-AZ80 heterogeneous alloy welding joint into a low-temperature environment box, controlling the cooling rate at 15 ℃/min, finally cooling to-165 ℃, processing for 7h, and then recovering to the room temperature at the heating rate of 20 ℃/min;
(8) after the treatment is finished, finally, the 5754-AZ80 heterogeneous alloy welding joint is taken out, the tensile property is tested, the tensile strength reaches 92.6MPa, and the test results are shown in Table 1.
Comparative example 1
The 5052-AZ31 hetero-alloy welded joint is only subjected to laser shock surface strengthening: the 5052-AZ31 hetero-alloy welded joint with the same batch, the same size and the same welding process as the plate in the example 1 is only subjected to laser shock surface strengthening, and the laser processing process is the same as the example 1. Then, the 5052-AZ31 hetero-alloy welded joint was subjected to tensile property testing, and the test results are shown in Table 1. The tensile strength of the welded joint obtained in example 1 reached 89.3MPa, whereas that of the welded joint obtained in comparative example 1 was only 65.2MPa, which was significantly inferior to that of example 1. The wear resistance test was carried out under the same conditions, and the wear amount in example 1 was 13mg and that in comparative example 1 was 18mg (the test results are shown in table 1), therefore, the 5052-AZ31 hetero-alloy welded joint was relatively poor in performance compared to the inventive treatment method because only surface strengthening was carried out, the microstructure defects inside the welded joint were not improved, and the internal welding residual thermal stress was not effectively eliminated.
Comparative example 2
5754-AZ80 Heteroalloy welded joint was only treated at ultra low temperature: the 5754-AZ80 hetero-alloy welded joint with the same plate batch phase diagram, the same size and the same welding process as those of the plate in the embodiment 2 is only subjected to ultralow temperature treatment, and the ultralow temperature treatment process is the same as that of the embodiment 2. Tensile properties were then tested on the 5754-AZ80 alloploy solder joints, the results of which are shown in Table 1. The tensile strength of the welded joint obtained in example 2 reached 92.6MPa, whereas that of the welded joint obtained in comparative example 1 was only 61.4MPa, which was significantly inferior to that of example 1. The abrasion resistance test was performed under the same conditions, and the abrasion loss was 11mg in example 2 and 26mg in comparative example 2 (the test results are shown in table 1), so that, compared with the treatment method of the present invention, the 5754-AZ80 hetero-alloy welded joint was relatively poor in tensile properties and abrasion resistance because the ultra-low temperature treatment was performed only and the micro-structural defects on the surface and inside of the welded joint were not improved.
Although the specific embodiments of the present invention have been described with reference to the examples, the scope of the present invention is not limited thereto, and those skilled in the art will appreciate that various modifications and variations can be made without inventive effort by those skilled in the art based on the technical solution of the present invention.
TABLE 1
| Sample numbering | Tensile strength (MPa) | Amount of abrasion (mg) |
| Example 1 | 89.3 | 13 |
| Example 2 | 92.6 | 11 |
| Comparative example 1 | 65.2 | 18 |
| Comparative example 2 | 61.4 | 26 |
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (10)
1. An aluminum-magnesium heterogeneous alloy postweld treatment process is characterized in that: the method specifically comprises the following steps:
(1) carrying out surface treatment on the aluminum-magnesium heterogeneous alloy welding piece to remove oil stains and dirt;
(2) carrying out surface laser shock treatment on the aluminum-magnesium heterogeneous alloy welding piece with the treated surface;
(3) putting an aluminum-magnesium heterogeneous alloy welding piece into a warm isostatic pressing device, fixing by using a fixture, introducing inert gas for gas pressurization heat treatment, recovering the welding piece to room temperature along with a furnace after the treatment process is finished, releasing the inert gas, reducing the static pressure of a cavity, unloading the welding piece after the temperature is recovered to the room temperature, and taking out the welding piece;
(4) and after the warm isostatic pressing treatment is finished, gradually cooling the environment temperature of the cavity to ultralow temperature for ultralow temperature treatment, slowly recovering to room temperature after the ultralow temperature treatment is finished, and taking out the aluminum-magnesium heterogeneous alloy welding piece.
2. The process of claim 1, wherein: in the step (2), an Nd-YAG solid laser is adopted for laser shock, the energy of the laser is 2.5-7J, the wavelength is 1.064 mu m, the frequency is 0.4-1 Hz, and the diameter of a light spot is 2.5-6 mm.
3. The process of claim 1, wherein: in the step (3), the inert gas is helium, argon or nitrogen.
4. The process of claim 1, wherein: in the step (3), before the inert gas is introduced, the vacuum degree is pumped to below 15 mPa.
5. The process of claim 1, wherein: in the step (3), in the process of filling nitrogen into the cavity, the static gas pressure is controlled to be 60MPa, and after the temperature of the welding joint is stable, the static gas pressure is adjusted to be 100-200 MPa.
6. The process of claim 1, wherein: in the step (3), the warm isostatic pressing treatment time is 3-4 h.
7. The process of claim 1, wherein: in the step (3), the temperature of the warm isostatic pressing is determined according to the solid solution temperatures of different alloys, and the temperature below the solid solution temperature is selected to be 10-15 ℃ as the corresponding treatment temperature.
8. The process of claim 1, wherein: in the step (4), the temperature of the cavity is controlled by pumping liquid nitrogen, so that the temperature of the cavity is adjusted within the range from room temperature to-190 ℃.
9. The process of claim 1, wherein: in the step (4), the temperature control precision is +/-1 ℃, the temperature reduction rate is controlled to be 10-20 ℃/min, the ultralow temperature treatment temperature is-130 to-180 ℃, and the treatment time is 5-7 h.
10. Use of the aluminum-magnesium dissimilar alloy post-weld treatment process according to any one of claims 1 to 9 in the field of metal welding.
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| Application Number | Priority Date | Filing Date | Title |
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| CN202110129045.9A CN112894113A (en) | 2021-01-29 | 2021-01-29 | Aluminum-magnesium heterogeneous alloy post-welding treatment process and application thereof |
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