CN114000070A - Aluminum alloy hollow section, heat treatment method for inhibiting abnormal growth of longitudinal weld grains of aluminum alloy hollow section and application of aluminum alloy hollow section - Google Patents
Aluminum alloy hollow section, heat treatment method for inhibiting abnormal growth of longitudinal weld grains of aluminum alloy hollow section and application of aluminum alloy hollow section Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
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Abstract
The invention provides an aluminum alloy hollow section, and a heat treatment method and application for inhibiting abnormal growth of longitudinal weld grains of the aluminum alloy hollow section, wherein the method comprises the steps of sequentially carrying out homogenization treatment, flow division extrusion, online water quenching, intermediate annealing, offline solid solution and artificial aging treatment on an as-cast aluminum alloy blank to obtain an aluminum alloy hollow section with a uniform structure; according to the method, the intermediate annealing treatment is inserted before the off-line solid solution treatment, so that the strain energy stored in the fine-grained structure of the welding seam area of the sectional material is fully released, grains are initially and uniformly grown, and the grain growth driving force of the welding seam area is greatly reduced; simultaneously, the method induces the grain boundary to precipitate a part of pinning particles before solid solution, and blocks the grain boundary migration in subsequent solid solution treatment; the method effectively reduces the phenomenon of abnormal growth of crystal grains in the welding seam area of the sectional material in the solution treatment, namely obviously reduces the width of the coarse crystal area of the welding seam of the sectional material after the solution treatment; in a tensile experiment, the method effectively reduces the area of the brittle fracture zone of the section bar test sample, and improves the mechanical property of the section bar.
Description
Technical Field
The invention belongs to the technical field of heat treatment reinforced hollow aluminum alloy sections, and particularly relates to an aluminum alloy hollow section, a heat treatment method for inhibiting abnormal growth of crystal grains of a longitudinal weld joint of the aluminum alloy hollow section and application of the aluminum alloy hollow section, in particular to a heat treatment method for a light high-strength aluminum lithium alloy hollow section for aerospace.
Background
The rapid development in the fields of aerospace, rail transit and the like has increased the demand for lightweight high-strength structural materials. The 2xxx and 7xxx series aluminum alloy hollow section has the characteristics of high specific strength, weldability, corrosion resistance and the like, and has important application in the fields of aerospace, rail transit and the like. Hollow aluminum alloy sections are typically produced by a split-flow extrusion process. The blank is first split into several strands of metal in the die cavity via a splitting die, then converged and welded in a welding chamber and extruded out via a die orifice to form a hollow profile. Different strands of metal flow flowing through the surfaces of the shunt bridges in the extrusion die act under high temperature and high pressure in the welding chamber to form longitudinal welding seams through solid welding, so that the hollow section inevitably forms one or more longitudinal welding seams along the length direction. Due to the violent friction shearing action between the blank and the die in the shunting extrusion process, the deformation degree of a longitudinal welding seam area is high, dynamic recrystallization is easy to occur under high temperature and high pressure, namely, fine isometric crystals storing a large amount of denaturation performance are formed, and the isometric crystals are easy to grow abnormally in the subsequent solid solution high temperature process to form a welding seam coarse crystal area, so the longitudinal welding seam area of the aluminum alloy hollow section is often composed of fine dynamic recrystallization crystal grains.
At present, for heat treatment strengthening type 2xxx and 7xxx series aluminum alloy sections, the section obtained by shunting extrusion still needs to be subjected to off-line solution quenching after on-line quenching, and can be subjected to artificial aging treatment. In the solid solution treatment, the fine dynamic recrystallization grains in the longitudinal weld zone of the sectional material are easy to grow abnormally at high temperature to form local coarse grains. The local coarse grains can cause uneven precipitation of strengthening phases of the section in aging, and cause stress concentration at coarse grains of a welding seam of the section in the service process, thereby finally influencing the damage tolerance and the overall performance of the machine body structure. Therefore, the hollow aluminum alloy section containing the coarse grains cannot be applied to the field of aerospace with strict performance requirements, and a novel heat treatment method capable of inhibiting abnormal growth of longitudinal weld grains in solution treatment of the aluminum alloy section is urgently developed.
According to the theory of grain growth, there are two methods for controlling abnormal growth of grains, one is to increase pinning force by increasing secondary phase particles, and the other is to reduce the driving force for grain growth. The current research and invention about inhibiting abnormal growth of weld grains mainly focuses on the field of friction stir welding. Researches show that the addition of alloy elements in the friction stir welding process can promote the precipitation of secondary phase particles in a welding seam area, increase the pinning force and inhibit the abnormal growth of crystal grains in a welding core area in subsequent heat treatment. However, the hollow aluminum alloy section is produced in a closed shunting extrusion die, and the process is difficult to add additional alloy elements. Therefore, a novel heat treatment method is provided for solving the problem of abnormal growth of weld grains of the aluminum alloy hollow section. The annealing treatment can eliminate the residual stress of the deformed structure, improve the uniformity and the thermal stability of the structure and hopefully reduce the grain growth driving force of the welding seam area of the section.
At present, the production process flow adopted by the heat treatment reinforced aluminum alloy hollow section is generally as follows: blank homogenizing treatment → split extrusion → online quenching → offline solid solution → artificial aging, wherein the offline solid solution is one of the key steps for improving the mechanical property of the hollow profile. However, fine grains in the longitudinal weld zone of the hollow aluminum alloy profile grow abnormally in the off-line solid solution process, a large-area coarse grain zone is formed around the longitudinal weld, and finally, the uneven precipitation of the strengthening phase and the sudden drop of the local mechanical property of the profile in the aging process are caused, so that the requirement of the aerospace field on high-quality profiles can not be met.
Disclosure of Invention
Aiming at the defects of a heat treatment reinforced hollow aluminum alloy section in the prior art, in particular to a third-generation light-weight high-strength aluminum lithium alloy hollow section, the invention aims to provide an aluminum alloy hollow section, a heat treatment method for inhibiting abnormal growth of crystal grains of a longitudinal weld joint of the aluminum alloy hollow section and application thereof, namely, a novel heat treatment method for off-line solid solution and artificial aging after annealing is provided.
In order to achieve the above purpose, the solution of the invention is as follows:
the invention provides a heat treatment method for inhibiting abnormal growth of grains of a longitudinal weld joint of an aluminum alloy hollow profile, which comprises the following steps:
(1) homogenizing the as-cast aluminum alloy blank to eliminate dendritic segregation, carrying out isothermal flow division extrusion on the blank to obtain an aluminum alloy hollow section containing a longitudinal welding line, and carrying out online water quenching treatment on the aluminum alloy hollow section after passing through an extrusion die;
(2) carrying out intermediate annealing treatment with different parameters on the aluminum alloy hollow section subjected to online water quenching in the step (1), and cooling the section to room temperature after the annealing treatment;
(3) carrying out off-line solid solution treatment on the aluminum alloy hollow section subjected to annealing treatment and air cooling in the step (2) to obtain a supersaturated solid solution;
(4) carrying out metallographic observation on the supersaturated solid solution obtained in the step (3) to obtain the range of a coarse crystal area around a longitudinal weld joint of the supersaturated solid solution, thereby determining the range of intermediate annealing treatment parameters which have an inhibiting effect on abnormal growth of crystal grains of the longitudinal weld joint of the section;
(5) and (4) carrying out artificial aging treatment on the hollow section with the longitudinal weld seam grains not obviously growing abnormally to obtain the aluminum alloy hollow section with uniform structure and performance.
As a preferred embodiment of the present invention, in step (1), the temperature for homogenization is 450 ℃ to 550 ℃ for 20-26 h.
As a preferred embodiment of the present invention, in step (1), the temperature of the partial extrusion is 400-500 ℃ and the speed is 1-3 mm/s.
As a preferred embodiment of the present invention, in step (2), the annealing temperature is 400-525 ℃ and the annealing time is 0-72 h.
As a preferred embodiment of the invention, in the step (3), the temperature of off-line solid solution is 500-550 ℃, and the time is 70-100 min.
In step (4), the intermediate annealing treatment parameter range with the effect of inhibiting abnormal growth of weld grains is determined as a preferred embodiment of the invention: the annealing temperature is 450 ℃ and the annealing time is 12-36h, or the annealing temperature is 475 ℃ and the annealing time is 0-6 h.
As a preferred embodiment of the invention, in the step (4), the annealing temperature is 450 ℃, and the effect of inhibiting abnormal growth of weld grains is best when the annealing time is 24 hours.
As a preferred embodiment of the invention, in the step (5), the temperature of the artificial aging is 150-.
The second object of the present invention is to provide an aluminum alloy hollow section having a uniform microstructure, which is obtained by the above heat treatment method.
The invention further provides the aluminum alloy hollow section, which is applied to the aerospace field or the military field.
Due to the adoption of the scheme, the invention has the beneficial effects that:
firstly, in the heat treatment method, the intermediate annealing treatment is inserted before the off-line solid solution treatment, so that the strain energy stored in the fine crystal structure of the welding seam area can be fully released, and the crystal grains can grow uniformly primarily, thereby greatly reducing the growth driving force of the crystal grains, effectively reducing the abnormal growth phenomenon of the crystal grains of the welding seam area of the sectional material in the subsequent solid solution treatment, namely reducing the width of the coarse crystal area of the welding seam in the subsequent solid solution treatment. Meanwhile, in a tensile experiment, the method effectively reduces the area of the brittle fracture zone of the profile, improves the mechanical property of the profile, and reduces the width of the coarse-grained brittle zone in the fracture of the profile, namely the ductility is obviously improved. Therefore, the abnormal growth of crystal grains of the aluminum alloy hollow section is inhibited, the novel light high-strength aluminum-lithium alloy section can be widely applied, and the further weight reduction of the aircraft structure is facilitated.
The invention provides a novel heat treatment method for annealing, off-line solid solution and artificial aging in sequence and an experimental method for determining process parameters, which can effectively inhibit the abnormal growth phenomenon of crystal grains of the section in the solid solution treatment process and reduce the width of a coarse crystal area of a welding seam of the section, thereby being suitable for hollow aluminum alloy sections containing longitudinal welding seams and obtained by different materials and different extrusion parameters and being also suitable for a friction stir welding joint with the similar welding seam coarse crystal problem.
Thirdly, the grain size of the welding seam area of the section is initially increased through annealing treatment, and the grain growth driving force is reduced; secondary phases can be precipitated during annealing, a certain pinning effect on a crystal boundary is achieved, and the stability of crystal grains in a welding seam area is improved; therefore, the annealing treatment part is introduced into the heat treatment of the aluminum alloy section so as to reduce the grain growth driving force at the welding seam of the section and reduce or even avoid the abnormal growth of the welding seam grains.
Fourthly, the method has simple process, easy operation and convenient industrial production, and is not limited by the shape and thickness of the extruded section. And the method can be easily realized under the original industrial production condition without new equipment investment.
Drawings
FIG. 1 is a gold phase diagram of a weld macrocrystalline region after different heat treatment processes in examples and comparative examples of the present invention.
FIG. 2 is a statistical chart of grain growth in the weld zone after annealing treatment in the embodiment of the present invention.
FIG. 3 is a statistical chart of the grain growth in the weld zone after annealing and solution treatment in the example of the present invention.
FIG. 4 is a schematic view of a heat treatment process according to an embodiment of the present invention.
FIG. 5 is a diagram showing the grain size and pinning particle distribution in the weld zone before and after annealing treatment in examples of the present invention and comparative examples.
FIG. 6 is a graph showing the microhardness, tensile property and fracture morphology of the profiles after different heat treatments in the examples of the present invention and the comparative examples.
Detailed Description
The invention provides an aluminum alloy hollow section, a heat treatment method for inhibiting abnormal growth of crystal grains of a longitudinal weld joint of the aluminum alloy hollow section and application of the heat treatment method.
< Heat treatment method for inhibiting abnormal growth of crystal grains in longitudinal weld joint of aluminum alloy hollow section >
The invention takes 2196Al-Cu-Li alloy as an example to introduce the concrete steps and the basic principle of the invention. The 2196Al-Cu-Li alloy used had a composition of 0.32 wt% Ag, 3.00 wt% Cu, 1.4 wt% Li, 0.42 wt% Mg, 0.26 wt% Zn and 0.11 wt% Zr, with the balance being Al.
The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow section comprises the following steps:
(1) blanking a 2196 aluminum-lithium alloy bar obtained by semi-continuous casting to obtain a cylindrical blank with the diameter of about 120cm and the height of 140cm, placing the blank into a muffle furnace at 500 ℃ for homogenization treatment for 24 hours, and then taking out for air cooling;
(2) heating the blank after air cooling to the deformation temperature of 470 ℃ and preserving heat for 2h, placing the extrusion die in a heating furnace to heat to 450 ℃ and preserving heat for 2h, simultaneously starting a heating device on an extruder, and similarly preheating an extrusion cylinder to 450 ℃ and preserving heat for 2 h;
(3) placing the preheated extrusion die and the blank in an 800t horizontal extruder to complete a shunting extrusion experiment to obtain an aluminum lithium alloy plate with the cross section size of 60 x 4, wherein the center of the plate is provided with a longitudinal welding line penetrating through the length direction of the section bar, and when the plate flows out of the extrusion die, an online quenching system on the extrusion device is started to perform online water quenching on the plate;
(4) and cutting the quenched plate along the extrusion direction to obtain a blocky heat treatment sample and a standard tensile sample, so that the positions of the samples can span the longitudinal welding line, the size of the blocky sample along the extrusion direction perpendicular to the samples is not less than 20mm, and the welding line is positioned in the center of the sample. And performing intermediate annealing treatment and off-line solution treatment by adopting a tubular furnace, and performing artificial aging treatment by adopting an oil bath furnace.
Wherein, in the step (1), the temperature for homogenization can be 450-550 ℃, preferably 500 ℃; the time can be 20-26h, preferably 24 h.
In the step (2), the annealing temperature is 400-525 ℃ and the annealing time is 0-72 h.
In the step (3), the temperature of the shunt extrusion can be 400-; the rate may be 1-3mm/s, preferably 2 mm/s.
In the step (4), determining the intermediate annealing treatment parameter range with the function of inhibiting abnormal growth of weld grains: the annealing temperature is 450 ℃ and the annealing time is 12-36h, or the annealing temperature is 475 ℃ and the annealing time is 0-6 h.
In the step (4), the annealing temperature is preferably 450 ℃, and the effect of inhibiting abnormal growth of weld grains is best when the annealing time is preferably 24 hours.
In the step (4), the temperature of the off-line solid solution can be 500-550 ℃, preferably 515 ℃; the time can be 70-100min, preferably 90 min.
In the step (4), the temperature of the artificial aging may be 150-; the time may be 22-26h, preferably 24 h.
< hollow aluminum alloy section >
The aluminum alloy hollow section bar is obtained by the heat treatment method.
< application of hollow aluminum alloy section >
The aluminum alloy hollow section bar can be applied to the aerospace field or the military field.
As mentioned above, the conventional heat treatment method for the aluminum alloy hollow section can cause abnormal growth of crystal grains at the longitudinal weld joint, so that the performance of the aluminum alloy hollow section is reduced, and the aluminum alloy hollow section can not meet the strict requirements in the aerospace field. In order to solve the above technical problems, the technical contents of the present invention will be further described below with reference to examples and comparative examples. The following examples are illustrative and not intended to be limiting, and are not intended to limit the scope of the invention. The experimental procedures used in the following examples are all conventional procedures unless otherwise specified. Materials, reagents and the like used in the following examples are commercially available unless otherwise specified.
Comparative example 1:
influence of common peak aging treatment (T6) on abnormal growth behavior and mechanical property of longitudinal weld grains of the 2196Al-Cu-Li alloy section.
(1) Blanking a 2196 aluminum lithium alloy bar obtained by semi-continuous casting to obtain a cylindrical blank with the diameter of about 120cm and the height of 140cm, putting the blank into a muffle furnace at 500 ℃, preserving heat for 24 hours at 500 ℃, and then taking out for air cooling.
(2) Heating the blank after air cooling to 470 ℃ of deformation temperature and preserving heat for 2h, placing the extrusion die in a heating furnace to 450 ℃ and preserving heat for 2h, simultaneously starting a heating device on the extruder, and preheating the extrusion cylinder to 450 ℃ and preserving heat for 2 h.
(3) And placing the preheated extrusion die and the blank in an 800t horizontal extruder, setting the extrusion temperature to be 450 ℃, the extrusion speed to be 2mm/s, completing a shunting extrusion experiment to obtain the aluminum-lithium alloy plate with the cross section size of 60 x 4, wherein the center of the plate is provided with a longitudinal welding line penetrating through the length direction of the section, and the plate flows out of the extrusion die and simultaneously starts an online quenching system on the extrusion device to perform online water quenching on the plate.
(4) And cutting the quenched plate into a blocky heat treatment sample and a standard tensile sample along the extrusion direction, so that the positions of the samples can span the longitudinal welding line, the size of the samples along the direction perpendicular to the extrusion direction is not less than 20mm, and the welding line is positioned in the center of the sample. And carrying out aging treatment by adopting solution treatment and an oil bath furnace.
And putting the block sample for microstructure observation and the tensile sample for mechanical property test after on-line quenching into a tubular furnace for solution treatment, namely keeping the furnace temperature at 515 ℃ for 90min, immediately taking out the sample, putting the sample into cold water for quenching, and ensuring that the quenching transfer time of a single sample is less than 5 s. The sample after solid solution was mechanically polished until the surface of the sample became a mirror surface, and then the surface of the sample was corroded with a kele reagent, and the width of the coarse crystal region was determined to be about 15mm under a metallographic microscope, as shown in fig. 1 (a).
And (3) performing peak aging treatment on the block sample and the tensile sample after the solution treatment, namely placing the block sample and the tensile sample in an oil bath furnace at 170 ℃ for 24 hours, taking out the block sample and the tensile sample, and cooling the block sample and the tensile sample to room temperature. And similarly, polishing and corroding the block sample, determining the width of a coarse crystal region, and carrying out mechanical property test and fracture morphology observation on the tensile sample.
Example 1:
the annealing treatment has the inhibiting effect on the abnormal growth behavior of the crystal grains of the longitudinal weld of the 2196Al-Cu-Li alloy section and the influence on the mechanical property of the section.
(1) Blanking a 2196 aluminum lithium alloy bar obtained by semi-continuous casting to obtain a cylindrical blank with the diameter of about 120cm and the height of 140cm, putting the blank into a muffle furnace at 500 ℃, preserving heat for 24 hours at 500 ℃, and then taking out for air cooling.
(2) Heating the blank after air cooling to 470 ℃ of deformation temperature and preserving heat for 2h, placing the extrusion die in a heating furnace to 450 ℃ and preserving heat for 2h, simultaneously starting a heating device on the extruder, and preheating the extrusion cylinder to 450 ℃ and preserving heat for 2 h.
(3) And placing the preheated extrusion die and the blank in an 800t horizontal extruder, setting the extrusion temperature to be 450 ℃, the extrusion speed to be 2mm/s, completing a shunting extrusion experiment to obtain the aluminum-lithium alloy plate with the cross section size of 60 x 4, wherein the center of the plate is provided with a longitudinal welding line penetrating through the length direction of the section, and the plate flows out of the extrusion die and simultaneously starts an online quenching system on the extrusion device to perform online water quenching on the plate.
(4) And cutting the quenched plate into a blocky heat treatment sample and a standard tensile sample along the extrusion direction, so that the positions of the samples can span the longitudinal welding line, the size of the samples along the direction perpendicular to the extrusion direction is not less than 20mm, and the welding line is positioned in the center of the sample.
And putting the block sample subjected to on-line quenching into a tubular furnace for annealing treatment. In this embodiment, a traversal annealing experiment is performed in a larger range to determine the range of annealing parameters that do not cause abnormal grain growth. Wherein the annealing temperature is set to 400-525 ℃, the time is 0-72h, and the temperature interval is 25 ℃. And air-cooling the annealed block samples to room temperature, polishing and corroding each sample, and observing the range of a coarse crystal area of a welding seam. In the embodiment, the welding seam coarse grain region is specified to be a complete abnormal grain growth region when the width of the welding seam coarse grain region is 10-15mm, the welding seam coarse grain region is specified to be a partial abnormal grain growth region when the width of the welding seam coarse grain region is less than 10mm, and the welding seam coarse grain region without abnormal grain growth completely does not occur. As shown in figure 2, abnormal grain growth does not occur at all when the annealing temperature of the section is below 450 ℃, and abnormal grain growth does not occur in the weld zone when the heat preservation time is between 0 and 12 hours when the annealing temperature is 450 ℃. The annealing temperature is 450 ℃, the heat preservation time is 12-36h, the primary crystal grains in the welding seam area of the section bar are abnormally grown, but the width of the coarse crystal area is less than 10 mm. Similarly, when the annealing temperature is 475 ℃ and the heat preservation time is 0-6h, a coarse crystal area with the width less than 10mm appears in the welding seam area of the section, and the phenomenon of abnormal growth of crystal grains at the welding seam part appears. Therefore, the temperature range between 450 ℃ and 475 ℃ is a temperature range for inducing abnormal growth of weld grains, the abnormal growth of part of the grains in the weld zone of the profile is caused when the heat treatment parameter ranges from 450 ℃/12 h to 36h and 475 ℃/0 h to 6h, and the complete abnormal growth of the grains in the weld zone is caused when the temperature is continuously increased or the annealing heat preservation time is continuously prolonged on the basis.
And (3) putting the block sample with the annealed weld grains not completely growing abnormally into a 515 ℃ tube furnace, preserving the heat for 90min, then immediately taking out and quenching, wherein the quenching transfer time is less than 5 s. And (3) polishing and metallographic observation are carried out on the annealed and solid-dissolved sample, and the width change of a coarse crystal area of the welding seam is determined, as shown in figure 3. The original sample without the abnormal grain growth area in fig. 2 has abnormal grain growth in the subsequent solution treatment, and the coarse grain area is widened to 15mm, so that the complete abnormal grain growth occurs. The annealing parameter ranges are 450 ℃/12-36h and 475 ℃/0-6h, namely the width of a coarse crystal area of a sample with abnormal growth of a welding seam crystal grain in annealing is slightly expanded in subsequent solution treatment, but the width of the coarse crystal area is far less than 10 mm. Therefore, the annealing treatment parameter ranges for inhibiting the abnormal growth phenomenon of longitudinal weld grains of the 2196 aluminum lithium alloy shunt extrusion section obtained under the extrusion process conditions of 450 ℃ and 2mm/s are 450 ℃/12-36h and 475 ℃/0-6 h.
Preferably, the temperature range of the intermediate annealing treatment is about 30-50 ℃ lower than the solid solution temperature, so as not to cause abnormal growth of the weld grains of the section.
Further preferably, the 450 ℃ intermediate annealing treatment is carried out for 12-36 hours, and the time is longer than 12 hours to fully reduce the grain growth driving force of the weld zone fine crystalline structure, so as to achieve the purpose of inhibiting the abnormal grain growth in the subsequent solid solution treatment; but after the time is longer than 36 hours, the abnormal growth of crystal grains occurs in the section sample in the annealing stage, and the coarse crystal area is expanded to about 15mm, so that the effect of inhibiting the abnormal growth of the crystal grains in the subsequent solid solution treatment cannot be achieved.
Further preferably, the annealing parameters with the most significant inhibition effect are 450 ℃ and 24h, as shown in (d) of FIG. 1. After the intermediate annealing treatment at 450 ℃ for 24 hours, the width of the coarse crystal zone of the welding seam of the sample is 1.5mm, and then the coarse crystal zone of the welding seam is expanded to 2mm (as shown in (e) in figure 1) after the solid solution treatment and the water quenching treatment at 515 ℃ for 90 minutes, compared with the sample with 15mm coarse crystal zone in comparative example 1, the width of the coarse crystal zone of the welding seam is reduced by nearly 90%.
And (3) carrying out artificial aging treatment on the sample subjected to the intermediate annealing treatment and the solution treatment at 450 ℃ for 24 hours, namely, placing the sample in an oil bath furnace at 170 ℃ for 24 hours, taking out the sample, and cooling the sample to room temperature in air.
The heat treatment process flow is shown in figure 4, and the method can effectively reduce the width of the coarse crystal area of the welding seam of the aluminum alloy section caused by the solution treatment. FIG. 5 shows the grain morphology and the pinning particle distribution of the block-shaped test sample of the extruded section weld and the test sample after annealing treatment at 450 ℃ for 24 h. As can be seen from (a) and (b) in FIG. 5, after annealing, grains in the weld zone of the profile are initially and uniformly grown, and the average size of the grains is increased. As can be seen from (c) and (d) in fig. 5, during the annealing process, the weld zone precipitates a large amount of secondary phase particles distributed on the grain boundaries, and these particles can effectively pin the grain boundaries and inhibit grain boundary migration. Therefore, after annealing treatment, on one hand, the grain size of the sample is preliminarily and uniformly grown, the growth driving force of the grains can be effectively reduced, on the other hand, a large number of secondary-phase pinning particles are precipitated in annealing, the grain boundary migration can be hindered, and the pinning force is improved. Due to the combined action of the two factors, abnormal growth of crystal grains is not easy to occur when the weld zone sample after annealing treatment is subjected to solution treatment.
And (4) polishing and corroding the block sample subjected to the aging treatment to determine the width of a coarse crystal area of the welding seam. And carrying out mechanical property test and fracture morphology observation on the time-lapse treated tensile sample to determine the influence of the novel heat treatment process on the mechanical property and the fracture behavior of the section.
The test piece in the weld zone, which was treated only by the T6 treatment of comparative example 1 (515 ℃, 90min solid solution +170 ℃, 24h aging), was found to have a tensile strength of 430MPa and a relatively poor elongation at break of only 6%. The tensile strength of the sample treated by the intermediate annealing treatment of 24 hours and T6 at 450 ℃ in the example 1 is increased by about 20MPa, the elongation at break is increased by about 2.5 percent, and the amplification can reach 42 percent.
Through the steps, the intermediate annealing heat treatment parameter range which corresponds to the hollow aluminum alloy section with different materials and different extrusion parameters and effectively inhibits the abnormal growth of the longitudinal weld grains can be obtained, and the novel heat treatment process method which can effectively improve the mechanical property of the section can be obtained.
FIG. 6 shows the appearance of fractures of samples aged by the conventional T6 peak in comparative example 1 and treated by the 24h annealing + T6 at 450 ℃ in example 1. As can be seen from the figure, the fracture of the weld zone sample after the T6 peak aging treatment is along-grain fracture, and after the treatment of annealing at 450 ℃ for 24h and T6, the area of the coarse crystal zone of the weld zone of the sample is reduced by about 90 percent, and the area of the dissociation/dimple fracture zone is obviously increased.
In conclusion, aiming at the problem that crystal grains in the longitudinal weld zone of the traditional aluminum alloy hollow section are easy to have local coarse grains in the heat treatment process, the invention provides a novel aluminum alloy section heat treatment method of intermediate annealing → offline solid solution → artificial aging. According to the method, through annealing treatment, unstable dynamic recrystallization small grains in a longitudinal weld zone of the aluminum alloy profile are promoted to grow uniformly primarily on the premise of not causing abnormal growth of grains in the weld zone and keeping the grain structures of other areas of the profile relatively stable, deformation energy and grain boundary energy stored in the aluminum alloy grains during shunting extrusion deformation are released, and the grain growth driving force of the profile to the weld zone is reduced; and simultaneously, partial secondary phase particles are precipitated on the crystal boundary, so that the migration of the crystal boundary is hindered, the abnormal growth of crystal grains of the hollow section in the subsequent heat treatment is inhibited, and the high-quality hollow aluminum alloy section with uniform crystal grain structure and mechanical property is favorably obtained. The method can effectively improve the mechanical property of the section and reduce the width of a coarse-grained brittle zone in a fracture of the section.
The previous description of the disclosed embodiments is provided to enable any person skilled in the art to make or use the present invention. It will be readily apparent to those skilled in the art that various modifications to these embodiments and the generic principles defined herein may be applied to other embodiments without the use of the inventive faculty. Therefore, the present invention is not limited to the above-described embodiments. Those skilled in the art should appreciate that many modifications and variations are possible in light of the above teaching without departing from the scope of the invention.
Claims (10)
1. A heat treatment method for inhibiting abnormal growth of grains of a longitudinal weld joint of an aluminum alloy hollow profile is characterized by comprising the following steps: which comprises the following steps:
(1) homogenizing the as-cast aluminum alloy blank, then carrying out isothermal flow division extrusion on the blank to obtain an aluminum alloy hollow section containing a longitudinal welding line, and carrying out online water quenching treatment on the aluminum alloy hollow section after passing through an extrusion die;
(2) carrying out intermediate annealing treatment on the aluminum alloy hollow section subjected to online water quenching in the step (1), and cooling the section to room temperature after annealing treatment;
(3) carrying out off-line solid solution treatment on the aluminum alloy hollow section subjected to annealing treatment and air cooling in the step (2) to obtain a supersaturated solid solution;
(4) carrying out metallographic observation on the supersaturated solid solution obtained in the step (3) to obtain the range of a coarse crystal area around a longitudinal weld joint of the supersaturated solid solution, thereby determining the range of intermediate annealing treatment parameters which have an inhibiting effect on abnormal growth of crystal grains of the longitudinal weld joint of the section;
(5) and (4) carrying out artificial aging treatment on the hollow section with the longitudinal weld seam crystal grains not obviously growing abnormally to obtain the aluminum alloy hollow section.
2. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (1), the temperature for homogenization is 450-550 ℃, and the time is 20-26 h.
3. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (1), the temperature of the flow-dividing extrusion is 400-500 ℃, and the speed is 1-3 mm/s.
4. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (2), the annealing temperature is 400-525 ℃ and the time is 0-72 h.
5. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (3), the temperature of the off-line solid solution is 500-550 ℃, and the time is 70-100 min.
6. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (4), determining the intermediate annealing treatment parameter range with the effect of inhibiting abnormal growth of weld grains: the annealing temperature is 450 ℃ and the annealing time is 12-36h, or the annealing temperature is 475 ℃ and the annealing time is 0-6 h.
7. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (4), the effect of inhibiting abnormal growth of weld grains is good when the annealing temperature is determined to be 450 ℃ and the annealing time is 24 hours.
8. The heat treatment method for inhibiting the abnormal growth of the crystal grains of the longitudinal weld joint of the aluminum alloy hollow profile as claimed in claim 1, is characterized in that: in the step (5), the temperature of the artificial aging is 150-200 ℃, and the time is 22-26 h.
9. An aluminum alloy hollow section is characterized in that: obtained by the heat treatment method according to any one of claims 1 to 8.
10. Use of an aluminium alloy hollow profile according to claim 9 in the aerospace or military field.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117102654A (en) * | 2023-09-28 | 2023-11-24 | 南京工业大学 | Method for improving structural uniformity of friction stir additive manufacturing aluminum alloy |
Citations (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DD258027A1 (en) * | 1982-10-29 | 1988-07-06 | Mansfeld Kombinat W Pieck Veb | METHOD FOR THE HEAT TREATMENT OF AN ALSI 1 ALLOY |
| DE29914735U1 (en) * | 1999-08-23 | 1999-11-18 | Hoogovens Aluminium Profiltechnik Bonn GmbH, 53117 Bonn | Welded multi-chamber hollow profile |
| CA2399215A1 (en) * | 2000-12-13 | 2002-06-20 | The Furukawa Electric Co., Ltd | Method of manufacturing aluminum alloy fin material for brazing |
| US20040094245A1 (en) * | 2002-11-15 | 2004-05-20 | Zhong Li | Aluminum automotive frame members |
| EP1634670A1 (en) * | 2004-09-13 | 2006-03-15 | The Boeing Company | Method to improve properties of aluminium alloys processed by solid state joining |
| CN102191413A (en) * | 2011-06-27 | 2011-09-21 | 南通恒秀铝热传输材料有限公司 | Aluminum-steel composite new aluminum alloy special material for air cooling |
| US20130206274A1 (en) * | 2010-08-18 | 2013-08-15 | Huntington Alloys Corporation | Process for producing large diameter, high strength, corrosion-resistant welded pipe and pipe made thereby |
| CN105543742A (en) * | 2016-02-03 | 2016-05-04 | 中南大学 | Heat treatment technique of thick-wall aluminum alloy hollow extruded section |
| CN106378527A (en) * | 2016-09-28 | 2017-02-08 | 武汉理工大学 | Method for preventing abnormal grains of aluminium alloy friction stir welding connector from growing |
| CN107338404A (en) * | 2017-06-19 | 2017-11-10 | 北京科技大学 | It is a kind of to improve welded seam of aluminium alloy intensity and the method for anti-crack ability |
| CN109500121A (en) * | 2018-11-14 | 2019-03-22 | 山东大学 | Electric pulse assists hot-pressed device and manufacturing process |
| CN109955003A (en) * | 2019-03-27 | 2019-07-02 | 中国航发北京航空材料研究院 | High-strength, anti-corrosion Al-Mg-Zr aluminium alloy welding wire and preparation method thereof |
| CN110129640A (en) * | 2019-06-28 | 2019-08-16 | 江西理工大学 | A kind of increasing material manufacturing 7000 line aluminium alloy wire rods and preparation method thereof |
| CN110202865A (en) * | 2019-05-23 | 2019-09-06 | 江苏常铝铝业集团股份有限公司 | Ultra-thin resist collapse soldering aluminium alloy compound fin material and preparation method thereof |
| CN110205527A (en) * | 2019-06-28 | 2019-09-06 | 江西理工大学 | A kind of increasing material manufacturing Al-Mg-Si alloy wire rod and preparation method thereof |
| CN111057975A (en) * | 2019-12-23 | 2020-04-24 | 中国航空制造技术研究院 | Preparation method of aluminum-lithium alloy superplastic fine-grain plate |
| CN111549264A (en) * | 2020-06-17 | 2020-08-18 | 中铝萨帕特种铝材（重庆）有限公司 | Preparation process of high-strength corrosion-resistant 5383 aluminum alloy and marine section |
| CN113186387A (en) * | 2021-04-16 | 2021-07-30 | 上海交通大学 | Heat treatment method for inhibiting abnormal coarsening of crystal grains of Mg-Y-RE alloy repair welding joint |
-
2021
- 2021-11-02 CN CN202111287607.9A patent/CN114000070A/en active Pending
Patent Citations (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DD258027A1 (en) * | 1982-10-29 | 1988-07-06 | Mansfeld Kombinat W Pieck Veb | METHOD FOR THE HEAT TREATMENT OF AN ALSI 1 ALLOY |
| DE29914735U1 (en) * | 1999-08-23 | 1999-11-18 | Hoogovens Aluminium Profiltechnik Bonn GmbH, 53117 Bonn | Welded multi-chamber hollow profile |
| CA2399215A1 (en) * | 2000-12-13 | 2002-06-20 | The Furukawa Electric Co., Ltd | Method of manufacturing aluminum alloy fin material for brazing |
| US20040094245A1 (en) * | 2002-11-15 | 2004-05-20 | Zhong Li | Aluminum automotive frame members |
| EP1634670A1 (en) * | 2004-09-13 | 2006-03-15 | The Boeing Company | Method to improve properties of aluminium alloys processed by solid state joining |
| US20130206274A1 (en) * | 2010-08-18 | 2013-08-15 | Huntington Alloys Corporation | Process for producing large diameter, high strength, corrosion-resistant welded pipe and pipe made thereby |
| CN102191413A (en) * | 2011-06-27 | 2011-09-21 | 南通恒秀铝热传输材料有限公司 | Aluminum-steel composite new aluminum alloy special material for air cooling |
| CN105543742A (en) * | 2016-02-03 | 2016-05-04 | 中南大学 | Heat treatment technique of thick-wall aluminum alloy hollow extruded section |
| CN106378527A (en) * | 2016-09-28 | 2017-02-08 | 武汉理工大学 | Method for preventing abnormal grains of aluminium alloy friction stir welding connector from growing |
| CN107338404A (en) * | 2017-06-19 | 2017-11-10 | 北京科技大学 | It is a kind of to improve welded seam of aluminium alloy intensity and the method for anti-crack ability |
| CN109500121A (en) * | 2018-11-14 | 2019-03-22 | 山东大学 | Electric pulse assists hot-pressed device and manufacturing process |
| CN109955003A (en) * | 2019-03-27 | 2019-07-02 | 中国航发北京航空材料研究院 | High-strength, anti-corrosion Al-Mg-Zr aluminium alloy welding wire and preparation method thereof |
| CN110202865A (en) * | 2019-05-23 | 2019-09-06 | 江苏常铝铝业集团股份有限公司 | Ultra-thin resist collapse soldering aluminium alloy compound fin material and preparation method thereof |
| CN110129640A (en) * | 2019-06-28 | 2019-08-16 | 江西理工大学 | A kind of increasing material manufacturing 7000 line aluminium alloy wire rods and preparation method thereof |
| CN110205527A (en) * | 2019-06-28 | 2019-09-06 | 江西理工大学 | A kind of increasing material manufacturing Al-Mg-Si alloy wire rod and preparation method thereof |
| CN111057975A (en) * | 2019-12-23 | 2020-04-24 | 中国航空制造技术研究院 | Preparation method of aluminum-lithium alloy superplastic fine-grain plate |
| CN111549264A (en) * | 2020-06-17 | 2020-08-18 | 中铝萨帕特种铝材（重庆）有限公司 | Preparation process of high-strength corrosion-resistant 5383 aluminum alloy and marine section |
| CN113186387A (en) * | 2021-04-16 | 2021-07-30 | 上海交通大学 | Heat treatment method for inhibiting abnormal coarsening of crystal grains of Mg-Y-RE alloy repair welding joint |
Non-Patent Citations (6)
| Title |
|---|
| XIAO XU, XINWU MA: "Abnormal grain growth of 2196 Al-Cu-Li alloy weld seams during extrusion and heat treatment", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
| XIAO XU, XINWU MA等: "Effects of abnormal grain growth at longitudinal weld on the aging behavior and mechanical properties of 2196 AlACuALi alloy profile", 《MATERIALS & DESIGN》 * |
| XU,X等: "Effects of extrusion parameters and post -heat treatments on microstructures and mechanical properties of extrusion weld seams in 2195 Al -Li alloy profiles", 《JOURNAL OF MATERIALS RESEARCH AND TECHNOLOGY-JMR&T》 * |
| 季凯等: "新型高铜的6005A铝合金焊接接头疲劳性能", 《焊接学报》 * |
| 徐潇: "铝锂合金分流挤压型材纵向焊缝固态焊合行为及其组织与性能研究", 《万方数据库》 * |
| 徐潇: "铝锂合金分流挤压型材纵向焊缝固态焊合行为及其组织与性能研究", 《中国优秀博硕士学位论文全文数据库(博士)工程科技Ⅰ辑》 * |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN117102654A (en) * | 2023-09-28 | 2023-11-24 | 南京工业大学 | Method for improving structural uniformity of friction stir additive manufacturing aluminum alloy |
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