CN113061820A - Strengthening and toughening treatment process of ZL205A aluminum alloy - Google Patents
Strengthening and toughening treatment process of ZL205A aluminum alloy Download PDFInfo
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- CN113061820A CN113061820A CN202110327884.1A CN202110327884A CN113061820A CN 113061820 A CN113061820 A CN 113061820A CN 202110327884 A CN202110327884 A CN 202110327884A CN 113061820 A CN113061820 A CN 113061820A
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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
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0468—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment between cold rolling steps
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0081—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for slabs; for billets
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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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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Abstract
The invention discloses a strengthening and toughening treatment process of ZL205A aluminum alloy, belonging to the technical field of alloy preparation and comprising the following steps: s1, rolling the ZL205A aluminum alloy plate into 50% -85% of the original thickness at room temperature, and then recrystallizing and annealing the rolled plate at 350-550 ℃; repeating the rolling and recrystallization annealing processes for multiple times to obtain the ZL205A aluminum alloy plate with the total deformation of 27-75%; s2, placing the plate subjected to the S1 treatment at 450-550 ℃ for heat preservation, and preparing a toughened ZL205A aluminum alloy plate; the invention leads ZL205A to be obtained through multiple cold rolling recrystallization annealing treatment and solution treatmentAlloy Al2The Cu phase is obviously refined, and the strength and the plasticity of the alloy material are improved.
Description
Technical Field
The invention belongs to the technical field of alloy preparation, and particularly relates to a strengthening and toughening treatment process of ZL205A aluminum alloy.
Background
Among the non-ferrous metals, aluminum and aluminum alloys are the most commonly used metal structural materials. However, commercially pure aluminum has low strength and is not suitable for bearing structural members, and a certain proportion of alloying elements are usually added to pure aluminum, so that an aluminum alloy with high strength and good castability is obtained. Aluminum alloys can be classified into cast aluminum alloys and wrought aluminum alloys according to the forming process, wherein cast aluminum alloys refer to aluminum alloys for manufacturing parts or blanks by casting methods such as gravity casting or die casting. The cast aluminum alloy contains more alloy elements, and accounts for 5-25% of the total mass fraction. As a representative high-strength cast aluminum alloy, the Al-Cu alloy has higher strength, excellent plasticity and toughness, high-temperature performance and cutting processing performance, and is widely applied to the fields of aerospace, automobile manufacturing, mechanical electronics, building materials, ships and the like.
The Al-Cu series high-strength cast aluminum alloy is more in variety, and is typically represented by ZL205A alloy. The comprehensive performance of the ZL205A alloy comprehensively surpasses that of the international similar alloys, and makes great contribution to the development of aerospace, civil industry and the like in China. However, due to the factors of complex composition, wide crystallization temperature range, difficult control of the casting forming process and the like of the ZL205A alloy, casting defects such as inclusions, cracks, shrinkage cavities and the like are easily generated in the smelting process of the alloy, so that the casting performance of the alloy is difficult to meet the service requirement.
The ZL205A aluminum alloy generally consists of a softer alpha-Al matrix phase and a harder Al matrix phase2A Cu second phase composition. Wherein, the grain size and the distribution of the second phase have important influence on the mechanical property of the alloy. With the development of society, people begin to try to improve the microstructure of cast aluminum alloy by various processing methods, so as to improve the mechanical property of the cast aluminum alloy. The grain refining effect of modification treatment is obvious, but the variety and the process of the modifier need to be changed according to aluminum alloys with different grades; the process required by the rapid solidification technology is complex, the preparation cost is high, and the application in actual production is less; semi-solid metal working technology shapingThe process is complex and the production cost is high; after the solution treatment and the aging treatment, although the strength and the plasticity can be obviously improved, the grain structure after the treatment is coarser compared with the thermal mechanical treatment; the Equal Channel Angular Pressing (ECAP) technology cannot deform strongly and plastically at room temperature because the alloy is too brittle, and must be carried out at high temperature, so that the energy consumption is large.
In conclusion, the existing casting processes have certain defects in the aspect of regulating and controlling the mechanical properties of the ZL205A aluminum alloy, and further research is needed to effectively improve the mechanical properties of the ZL205A aluminum alloy by a simple means.
Disclosure of Invention
In order to solve the problems, the invention provides a strengthening and toughening treatment process of ZL205A aluminum alloy, which can improve the microstructure in ZL205A alloy and improve the plasticity and strength of the ZL205A alloy by multiple rolling and recrystallization annealing and solid solution strengthening; the cold rolling process can improve the mechanical property and the rolled piece quality of the plate, is suitable for industrial mass production, and has wide application range, but the cast ZL205A alloy has casting defects and segregation, has poor cold plastic deformation capability and is easy to crack; according to the invention, through multiple cold rolling, crystal grains are continuously refined, an isomeric structure is generated, the mechanical property is improved, and meanwhile, the superstrong aluminum-copper alloy can be obtained by combining solid solution strengthening, precipitation strengthening and dislocation strengthening means on the basis, and the method is realized by the following scheme:
a strengthening and toughening treatment process of ZL205A aluminum alloy comprises the following steps:
s1, multiple cold rolling and recrystallization annealing treatment
Rolling a ZL205A aluminum alloy plate into 50% -85% of the original thickness at room temperature, and then recrystallizing and annealing the rolled plate at 350-550 ℃; repeating the rolling and recrystallization annealing processes for multiple times to obtain the ZL205A aluminum alloy plate with the total deformation of 27-75%;
s2 solution treatment
And (3) insulating the plate subjected to the S1 treatment at 450-550 ℃ to obtain the toughened ZL205A aluminum alloy plate.
Preferably, the method further comprises pre-straining and aging treatment, and specifically comprises the following steps:
rolling the toughened ZL205A aluminum alloy plate of S2 to 80-95% of the thickness of the S2 plate at room temperature or in a liquid nitrogen environment, and then carrying out aging annealing treatment on the plate at 150-230 ℃ to obtain the ultrahigh-strength aluminum alloy.
Preferably, in S1, the time of the recrystallization annealing treatment is 10 to 180 min.
Preferably, in S1, the rolling and recrystallization annealing processes are repeated 1 to 4 times.
Preferably, in S2, the heat preservation time is 0.5-3 h.
Preferably, the time of the aging annealing is 0.5-12 h.
Compared with the prior art, the invention has the following beneficial effects:
(1) the invention utilizes the method of multiple rolling and recrystallization annealing combined with solution treatment to continuously refine the crystal grains of the ZL205A aluminum alloy, and generates an isomeric structure, and the microstructure is improved, namely the structure of the as-cast ZL205A alloy which is not subjected to the treatment is composed of a coarse alpha matrix and coarse Al distributed along the crystal2The ZL205A alloy Al consisting of Cu phase and subjected to multiple cold rolling recrystallization annealing treatment and solution treatment of the invention2The Cu phase is obviously refined, so that the strength and the plasticity of the alloy material are improved;
(2) on the basis, the pre-strain and aging treatment are carried out, so that the strength of the alloy can be obviously improved, and different requirements on high plasticity or high strength of the aluminum alloy under different conditions can be met;
(3) the invention has simple process and low production cost, can meet different requirements on high plasticity or high strength of ZL205A aluminum alloy in different environments, and is suitable for popularization and application.
Drawings
FIG. 1 is a microstructure of aluminum alloys of comparative example 1 and example 2; wherein (a) is a photograph of a metallographic structure of a microscope of comparative example 1, and (b) and (c) are a scanning electron micrograph and a back-scattered electron diffraction pattern, respectively, of example 2;
fig. 2 is a tensile stress strain curve for the aluminum alloys of comparative example 1, example 2, and example 3, example 5.
Detailed Description
In order to make the technical solutions of the present invention better understood and implemented by those skilled in the art, the present invention is further described below with reference to the following specific embodiments and the accompanying drawings, but the embodiments are not meant to limit the present invention.
The experimental methods and the detection methods described in the following examples are all conventional methods unless otherwise specified; the reagents and materials are commercially available, unless otherwise specified.
Example 1
A strengthening and toughening treatment process of ZL205A aluminum alloy comprises the following steps:
s1, multiple cold rolling and recrystallization annealing treatment
A commercial ZL205A alloy 10mm thick plate is subjected to multi-pass rolling to 70% of the original thickness by a cold rolling mill at room temperature; then, carrying out recrystallization annealing on the rolled alloy at 400 ℃, keeping the temperature for 60min, taking out, and carrying out water cooling quenching; the cold rolling and recrystallization annealing processes are repeated for 1 time for the cooled sample, and compared with the original plate, the ZL205A (with the thickness of 4.9mm) aluminum alloy plate with the deformation of 51% is finally obtained;
s2 solution treatment
And (3) carrying out solution treatment on the aluminum alloy plate obtained in the step S1 at the temperature of 500 ℃, keeping the temperature for 2h, taking out the aluminum alloy plate, and carrying out water-cooling quenching to obtain the strengthening and toughening ZL205A alloy.
Example 2
A strengthening and toughening treatment process of ZL205A aluminum alloy comprises the following steps:
s1, multiple cold rolling and recrystallization annealing treatment
A 30mm thick plate made of commercial ZL205A alloy is subjected to multi-pass rolling to 70% of the original thickness by a cold rolling mill at room temperature; then, carrying out recrystallization annealing on the rolled alloy at the temperature of 420 ℃, keeping the temperature for 90min, taking out, and carrying out water cooling quenching; the cold rolling and recrystallization annealing processes are repeated for 2 times on the cooled sample, and compared with the original plate, the ZL205A (with the thickness of 10.29mm) aluminum alloy plate with the deformation of 65.7% is finally obtained;
s2 solution treatment
And (3) carrying out solution treatment on the aluminum alloy plate obtained in the step S1 at the temperature of 530 ℃, keeping the temperature for 1h, taking out the aluminum alloy plate, and carrying out water-cooling quenching to obtain the strengthening and toughening ZL205A alloy.
Example 3
The aluminum alloy sheet obtained in example 1 was cold rolled at room temperature to 90% of the thickness of the sheet treated in example 1, and then the alloy after rolling was subjected to aging annealing at 180 ℃, and after heat preservation for 1 hour, the sheet was taken out and water-cooled and quenched to obtain a pre-strained and aged ZL205A alloy.
Example 4
The aluminum alloy sheet obtained in example 2 was cold rolled at room temperature to 80% of the thickness of the sheet treated in example 2, and then the rolled alloy was subjected to aging annealing at 160 ℃, kept warm for 2 hours, taken out, and water-cooled quenched to obtain a pre-strained and aged ZL205A alloy.
Example 5
The aluminum alloy plate obtained in example 2 was subjected to low-temperature rolling at a liquid nitrogen temperature to a thickness of 95% of the plate treated in example 2, and then the rolled alloy was subjected to aging annealing at 160 ℃, and after heat preservation for 2 hours, the alloy was taken out and subjected to water-cooling quenching to obtain a pre-strained and aged ZL205A alloy.
Example 6
The plate in the example 1 is subjected to multiple cold rolling and recrystallization annealing treatments, and finally the ZL205A aluminum alloy plate with the deformation of 27% is obtained; the temperature of recrystallization annealing was 350 ℃ and the time was 180min, and the rest of the procedure was the same as in example 1.
Example 7
The plate in the example 1 is subjected to multiple cold rolling and recrystallization annealing treatments, and finally the ZL205A aluminum alloy plate with the deformation of 75% is obtained; the temperature of recrystallization annealing was 550 ℃ and the time was 10min, and the rest of the procedure was the same as in example 1.
Example 8
The plate in the example 3 is subjected to aging annealing at the temperature of 150 ℃ and is kept warm for 12h, and the rest steps are the same as those in the example 3.
Example 9
The plate in the example 3 is subjected to aging annealing at 230 ℃ and heat preservation for 0.5h, and the rest steps are the same as those in the example 3.
Comparative example 1
Commercial cast aluminum alloy ZL205A panels.
The alloy materials prepared in the examples 1, 6 and 7 have the performance similar to that of the example 2, the alloy materials prepared in the examples 4, 8 and 9 have the performance similar to that of the example 3, and the alloy materials are subjected to relevant performance characterization by only taking the examples 2, 3, 5 and 1 as examples.
First, we compared the as-cast structure of a cast aluminum alloy ZL205A plate and the structure of ZL205A alloy after multiple cold rolling and recrystallization treatments, i.e., the microstructure of the ZL205A alloy of comparative example 1 and example 2, and fig. 1(a) is a photo-microscopic metallographic structure photograph of comparative example 1, and fig. 1(b) and fig. 1(c) are a scanning electron microscope picture and a back-scattered electron diffraction pattern of example 2, respectively. In FIG. 1(a), it can be seen that the as-cast ZL205A alloy had a structure consisting of a coarse alpha matrix and coarse Al along the grain distribution2ZL205A alloy Al consisting of Cu phase and subjected to multiple cold rolling recrystallization treatments and solution treatments2The Cu phase is obviously refined (shown in figure 1(b) and figure 1 (c)), which shows that the microstructure of the cast aluminum alloy can be obviously improved by the multiple cold rolling recrystallization treatment and solution treatment process of the invention.
Next, we tested the room temperature tensile properties of the aluminum alloys of example 2, example 3, example 5, and comparative example 1 after multiple rolling plus recrystallization and solution treatment, pre-strain and aging treatment, and as-cast, and fig. 2 is the corresponding tensile stress-strain curve. The tensile strength of the as-cast ZL205A alloy (comparative example 1) is about 225MPa, the performance of the cast aluminum alloy can be obviously improved by the multiple cold rolling, recrystallization and solution treatment process (example 2) of the invention, and compared with the comparative example 1, the plasticity and the strength are improved, the corresponding tensile strength can reach 350MPa, and the tensile plasticity is 37 percent; further, the tensile strength of the sample after being subjected to pre-strain and aging at room temperature (example 3) is further improved, and the maximum tensile plasticity can reach about 750MPa in a liquid nitrogen environment (example 5), and the tensile plasticity is about 6%, so that the method can be suitable for environments with high requirements on material strength.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, it is intended that such changes and modifications be included within the scope of the appended claims and their equivalents.
Claims (6)
1. A strengthening and toughening treatment process of ZL205A aluminum alloy is characterized by comprising the following steps:
s1, multiple cold rolling and recrystallization annealing treatment
Rolling a ZL205A aluminum alloy plate into 50% -85% of the original thickness at room temperature, and then recrystallizing and annealing the rolled plate at 350-550 ℃; repeating the rolling and recrystallization annealing processes for multiple times to obtain the ZL205A aluminum alloy plate with the total deformation of 27-75%;
s2 solution treatment
And (3) insulating the plate subjected to the S1 treatment at 450-550 ℃ to obtain the toughened ZL205A aluminum alloy plate.
2. The strengthening and toughening treatment process of the ZL205A aluminum alloy according to claim 1, further comprising pre-straining and aging treatment, and specifically comprising the following steps:
rolling the toughened ZL205A aluminum alloy plate of S2 to 80-95% of the thickness of the S2 plate at room temperature or in a liquid nitrogen environment, and then carrying out aging annealing treatment on the plate at 150-230 ℃ to obtain the ultrahigh-strength aluminum alloy.
3. The strengthening and toughening treatment process of ZL205A aluminum alloy according to claim 1, wherein in S1, the time of recrystallization annealing treatment is 10-180 min.
4. The strengthening and toughening treatment process of ZL205A aluminum alloy according to claim 1, wherein in S1, the rolling and recrystallization annealing process is repeated for 1-4 times.
5. The strengthening and toughening treatment process of the ZL205A aluminum alloy according to claim 1, wherein the heat preservation time in S2 is 0.5-3 h.
6. The strengthening and toughening treatment process of the ZL205A aluminum alloy according to claim 2, wherein the time for aging annealing is 0.5-12 h.
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN113857250A (en) * | 2021-09-15 | 2021-12-31 | 昆明理工大学 | Method for preparing metal semi-solid slurry by multi-stage rolling-annealing SIMA method |
| CN114990397A (en) * | 2022-06-13 | 2022-09-02 | 昆明理工大学 | Method for strengthening ZL201 aluminum alloy based on cold deformation and solid solution aging |
| CN115821177A (en) * | 2022-11-29 | 2023-03-21 | 武汉大学 | Strengthening and toughening method for precipitation strengthening type aluminum alloy and application thereof |
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| CN115821177A (en) * | 2022-11-29 | 2023-03-21 | 武汉大学 | Strengthening and toughening method for precipitation strengthening type aluminum alloy and application thereof |
| CN115821177B (en) * | 2022-11-29 | 2024-01-05 | 武汉大学 | Precipitation strengthening type aluminum alloy strengthening and toughening method and application thereof |
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