CN109628861B - Heat treatment method for synchronously improving strength and elongation of 7-series aluminum alloy plate - Google Patents
Heat treatment method for synchronously improving strength and elongation of 7-series aluminum alloy plate 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
- 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
- C22F1/053—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 zinc as the next major constituent
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- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
Abstract
The invention relates to the technical field of aluminum alloy, in particular to a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate. The method takes a 7-series aluminum alloy hot rolled plate as a treatment object, and sequentially adopts solid solution treatment, pre-aging treatment, regression heating treatment and re-aging treatment; and (5) obtaining a product. When the aluminum alloy 7050 plate is subjected to the design process disclosed by the invention, the tensile strength of the obtained product is 565-590 MPa, the yield strength is 520-560 MPa, and the elongation is 20-23.5%. The invention can realize the simultaneous improvement of the strength and the elongation of the alloy. In addition, the invention uses a continuous heating mode, can save a large amount of time in the regression heat treatment stage, and improves the production efficiency.
Description
Technical Field
The invention relates to the technical field of aluminum alloy, in particular to a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate.
Background
The 7050 aluminum alloy belongs to high-strength corrosion-resistant aluminum alloy, has strong compression resistance and impact resistance and better corrosion resistance, and is mainly used in the fields of aerospace, industry, clamps, mechanical equipment, mold processing and the like. The 7050 alloy contains Zn 5.7-6.7, Cu 2.0-2.6, Mg 1.9-2.6 and small amount of Zr, Si and other elements, and its main strengthening phase is MgZn2The foreign research mainly changes the strengthening phase in the 7050 alloy by adjusting different heat treatment process parameters and methods, thereby improving the microstructure and achieving the purposes of improving the strength and the corrosion resistance.
For 7 series aluminum alloy, common aging means include single-stage aging, double-stage aging, non-isothermal aging, regression and reaging.
The single-stage aging, namely peak aging (T6), is designed according to the principle that the heat preservation is carried out for a long time at the temperature lower than the temperature for dissolving GP zones, so that solute atoms in the alloy are fully precipitated. The organization is characterized in that: a large number of GP zones and fine and dispersed semi-coherent eta' phases are distributed in the crystal grains, and precipitated phases on the crystal grain boundaries are thick and large eta phases and are distributed in a continuous chain shape. The alloy strength in a peak aging state reaches a peak value, but the distribution of precipitated phases on a crystal boundary is in a continuous chain shape, so that the corrosion resistance is poor, the elongation is low, and the application of the alloy is limited to a great extent.
The two-stage aging process is carried out in two stages: the aging temperature of the first stage is generally lower than the dissolving temperature of GP zones, the purpose is mainly nucleation, so that a large number of GP zones are separated out on a matrix, and organization preparation is made for the next stage; the aging temperature of the second stage is higher, if the GP zone formed in the first stage reaches the critical dimension, the GP zone can be taken as the core of the precipitated phase of the second stage to continue to precipitate and grow, namely, the GP zone enters the stabilization stage, and the eta' phase and the eta phase are gradually precipitated in the crystal grains along with the prolonging of the aging time. Compared with the structure in the peak aging state, the size of the precipitated phase is increased after bipolar aging, and the distribution is more uniform. Further, solute atoms at grain boundaries have relatively high energy and are easily precipitated from solid solutions, so that a larger η phase is precipitated at grain boundaries than in the grains, and the continuous chain state is changed into independent particles, thereby widening the precipitation-free precipitation zone at grain boundaries. The strength of the alloy with the structural characteristics is reduced by 10-15% compared with the peak aging state (T6), but the corrosion resistance can be obviously improved.
The non-isothermal ageing process features that the alloy is aged in continuously varying temperature field. The main performance is as follows: in a non-isothermal process, thermodynamic parameters of alloy precipitated phases change along with temperature, and the precipitated phases can exist stably in a certain period of time and can be dissolved in the next period of time. In addition, in the aging strengthening process, all precipitated phases need to form stable phases through a certain precipitation sequence. In the precipitation process, a series of metastable phases are mutually transformed, and the metastable phases with different sizes have complex competitive relationship, so that the precipitation behavior of the alloy is more complex and changeable. In 2007, Jmaes et al introduced the non-isothermal aging concept into the aging process of 7-series aluminum alloy, i.e., aging the alloy by continuous heating or cooling, studied the mechanical properties and conductivity of the alloy, and finally obtained excellent mechanical properties. In recent years, researchers in China have studied the non-isothermal aging behavior of 7-series aluminum alloys and the influence thereof on mechanical properties, and it is considered that the termination temperature of continuous temperature increase or decrease has a large influence on the alloy structure and properties. As the temperature increases, the metastable phase transformation sequence of the 7-series aluminum alloy is GP → eta' → eta.
Retrogression and re-aging RRA (retrogression and re-aging), which is defined as a tertiary aging, was proposed in 1974 by Israel aircraft to improve the corrosion resistance of 7-series aluminum alloys without reducing their strength. The core technology is that the aging process is carried out in three stages, namely a pre-aging stage, a regression stage and a reaging stage, wherein the key is regression treatment. The regression temperature is higher than the pre-aging temperature and the re-aging temperature, and a temperature rising and reducing process, namely a regression heating and cooling stage, is arranged in the regression stage. In the regression stage, the GP zone with the initial regression size smaller than the critical size is redissolved, the GP zone with the initial regression size larger than the critical size is converted into an eta 'phase, and the original eta' phase gradually grows up; along with the extension of the regression time, a new eta ' phase is separated out, the original eta ' phase gradually grows up and is partially converted into the eta phase, so that the volume fractions of the eta ' phase and the eta phase are increased; and continuously prolonging the regression time, and gradually coarsening precipitated phase particles. In the re-aging stage, the GP zone which is not re-dissolved is taken as the core of a new eta 'phase to promote the eta' phase to be continuously separated out; the supersaturated solid solution formed after cooling down the regression temperature is still precipitated according to the precipitation sequence, so that the volume fraction of GP zone and eta' phase is greatly increased compared with the volume fraction in the regression state, and the peak aging state level is basically reached. In 2004, Oliveira A.F. et al studied the regression and reaging treatments of 7050 alloy, and found that the strength of 7050 alloy after reaging reached the strength of T6 state after the alloy had undergone 40 minutes regression at 200 ℃. The main characteristic of the regression and re-aging treatment is that the stress corrosion resistance of the alloy is improved, and the strength of the alloy is not reduced. From the regression temperature, it can be achieved at different temperatures, with regression times varying from a few minutes to several hours. At present, the research on RRA treatment at home and abroad mainly focuses on the influence of regression temperature and regression time on the regression reaging effect. Few studies have reported on the effects of the heating rate and cooling mode on the texture and properties of the regressive/reaged state.
Disclosure of Invention
The invention aims to provide a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate.
The invention firstly tries to use a 7 series aluminum alloy hot rolled plate as a treatment object and sequentially adopts solid solution treatment, pre-aging treatment, regression heating treatment and re-aging treatment; the product with excellent performance is obtained.
The invention provides a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate, which takes a 7-series aluminum alloy hot rolled plate as a treatment object and sequentially adopts solid solution treatment, pre-aging treatment, regression heating treatment and re-aging treatment; obtaining a product;
the solid solution treatment comprises the following steps: preserving the heat for 1 to 3 hours at the temperature of 460 to 480 ℃, transferring the product into a cooling medium within 5 seconds, and quenching the product; the temperature of a cooling medium in the quenching process is 22-26 ℃;
the pre-aging treatment comprises the following steps: heating the plate subjected to the solution treatment to 115-130 ℃, preserving the temperature for 20-30 hours, transferring the plate into a cooling medium, and quenching; the temperature of a cooling medium in the quenching process is 22-26 ℃;
the regression heating treatment comprises the following steps: heating the pre-aged plate to a set temperature at a speed of 3-6 ℃/min, transferring the plate to a cooling medium within 10s, and cooling; the set temperature is 160-260 ℃;
the re-aging treatment comprises the following steps: and heating the plate subjected to the returning heating treatment to 115-130 ℃, preserving heat, performing aging treatment for 20-30 hours, and cooling.
Preferably, the invention relates to a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate, and the 7-series aluminum alloy hot-rolled plate comprises a 7050 aluminum alloy hot-rolled plate.
According to the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate, the thickness of the 7050 aluminum alloy hot-rolled plate is 1-3 mm. The invention realizes the great improvement of the strength and the elongation of the 7050 aluminum alloy thin plate under the synergistic effect of the condition parameters by strictly controlling the range of each process parameter.
As a preferable scheme, the invention discloses a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate, wherein the preparation process of the 7-series aluminum alloy hot rolled plate comprises the following steps: taking 7 series aluminum alloy as a raw material, heating the raw material, and then carrying out hot rolling, wherein the deformation of the hot rolling is more than or equal to 95%; the temperature is controlled to be 450-480 ℃ during hot rolling. When the method is applied in the process, the hot rolling is carried out, and then the air cooling is carried out to the room temperature.
Preferably, the invention relates to a heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate, and the cooling medium comprises water.
Preferably, the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate comprises the following steps: heating the pre-aged plate to a set temperature at a speed of 5 ℃/min, transferring the plate to a cooling medium within 5s, and cooling.
Preferably, the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate has the set temperature of 180-.
As a further preferable scheme, the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate has the set temperature of 188-; after reaching the set temperature, the mixture was transferred to water for cooling within 5 seconds. In the invention, during the regression heating treatment, particularly after the temperature is more than or equal to 160 ℃, the time in the temperature interval is controlled to be obtained, and preferably 5-8 min; when the time is too long, especially when the time is more than 35min, the elongation of the final product is attenuated.
According to the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate, when the aluminum alloy plate is a 7050 alloy plate, the tensile strength of the obtained product is 565-590 MPa, the yield strength is 520-560 MPa, and the elongation is 20-23.5%.
After optimization, according to the heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate, when the aluminum alloy plate is a 7050 alloy plate, the tensile strength of the obtained product is 575-590 MPa, the yield strength is 540-560 MPa, and the elongation is 20.5-23.5%.
The invention has the technical effects that: the hot rolling at the temperature of 460-480 ℃ can well reduce the work hardening, so that the deformed alloy plate has uniform thickness and does not crack, and the alloy plate is ensured to be smoothly rolled. Meanwhile, the alloy obtains better recovery and recrystallization effects in the hot rolling process, and the ductility of the alloy is ensured. After the solid solution treatment and the water quenching, trace precipitated phases existing in the alloy are dissolved back into the aluminum matrix as much as possible, so that the elements in the alloy are more uniformly distributed, and the uniform precipitation of the phases in the later aging treatment process is guaranteed; the pre-aging treatment after the solution treatment can generate a large amount of GP zones and a small amount of eta 'phase in the alloy, and the dissolution back of the eta' phase can be prevented after water cooling. In the regression heating stage, along with the rise of the regression temperature and the extension of the heating time, a GP zone larger than the critical dimension is converted into an eta ' phase, the original eta ' phase gradually grows up and is partially converted into an eta phase, so that the volume fractions of the eta ' phase and the eta phase are increased. In addition, in the regression heating stage, as the temperature is increased relative to the pre-aging, a part of deformation energy storage can be well released, a part of harmful texture is eliminated, and the ductility of the alloy is further improved. In the reaging stage for 20-30 hours, on one hand, the GP zone which is not redissolved can be ensured to be used as the core of a new eta 'phase, so that the eta' phase is continuously separated out, and on the other hand, the supersaturated solid solution formed under the regression condition can be separated out according to the sequence of supersaturated solid solution → vacancy-rich group → GP zone → eta 'phase → eta phase, so that the volume fractions of the eta' phase and the eta phase are greatly increased compared with the volume fraction of the regression state, and the ordered arrangement is formed. By the above working and heat treatment, the strength and elongation of the alloy can be simultaneously improved.
Drawings
FIG. 1 is a characteristic diagram of an intragranular precipitate phase and GP zone of a 7050 alloy after being subjected to regression heating according to the present invention;
FIG. 2 is a characteristic diagram of the intragranular precipitate phase of the 7050 alloy after being re-aged by the present invention.
Detailed Description
In order to further explain the present invention and to enable others skilled in the relevant art to better understand the invention, the following examples are given by way of illustration only, but the present invention is not limited to the following examples, and should not be construed as being limited to the scope of the present invention.
Example 1
Carrying out hot rolling deformation on the alloy at 460-480 ℃ with the reduction of 95%, heating the alloy at 470 ℃, carrying out solution treatment after heat preservation for 2 hours, and then quenching the alloy in water at 24 ℃ at room temperature, wherein the transfer time of the sample is required to be less than 5 seconds; immediately preserving the heat of the quenched alloy for 25 hours at the temperature of 115 ℃, performing pre-aging treatment, and cooling in water at the room temperature of 24 ℃ to ensure that the sample transfer time is less than 5 seconds. Heating the pre-aged alloy to 160 ℃ at a heating rate of 5 ℃ per minute, carrying out regression heating, and cooling in water at room temperature of 24 ℃, wherein the sample transfer time is required to be less than 5 seconds; and (3) preserving the heat of the regressed alloy for 20 hours at the temperature of 115 ℃, performing re-aging treatment, and finally performing air cooling. Under the process conditions, the 7050 alloy has the tensile strength of 577MPa, the yield strength of 530MPa and the elongation of 20 percent.
Example 2
Carrying out hot rolling deformation on the alloy at 460-480 ℃, wherein the reduction is 95%; heating the alloy at 475 ℃, preserving heat for 1 hour to carry out solution treatment, and then quenching the alloy in water at 25 ℃ at room temperature, wherein the sample transfer time is required to be less than 5 seconds; immediately preserving the heat of the quenched alloy for 24 hours at 120 ℃, performing pre-aging treatment, and cooling in water at 25 ℃ at room temperature, wherein the sample transfer time is required to be less than 5 seconds. Heating the pre-aged alloy to 190 ℃ at a heating rate of 5 ℃ per minute, performing regression heating, and cooling in water at room temperature of 25 ℃, wherein the sample transfer time is required to be less than 5 seconds; and (3) preserving the heat of the regressed alloy at 120 ℃ for 28 hours, performing re-aging treatment, and finally performing air cooling. Under the process condition, the tensile strength of the 7050 alloy is 588MPa, the yield strength is 558MPa, and the elongation is 23%.
Example 3
Carrying out hot rolling deformation on the alloy at 460-480 ℃, wherein the reduction is 95%; heating the alloy at 480 ℃, preserving heat for 1.5 hours to carry out solution treatment, and then quenching the alloy in water at 26 ℃ at room temperature, wherein the transfer time of a sample is required to be less than 5 seconds; immediately preserving the heat of the quenched alloy at 120 ℃ for 28 hours, performing pre-aging treatment, and cooling in water at 25 ℃ at room temperature, wherein the sample transfer time is required to be less than 5 seconds. Heating the pre-aged alloy to 220 ℃ at a heating rate of 5 ℃ per minute, performing regression heating, and cooling in water at the room temperature of 26 ℃, wherein the sample transfer time is required to be less than 5 seconds; and (3) preserving the heat of the regressed alloy for 24 hours at the temperature of 120 ℃, performing re-aging treatment, and finally performing air cooling. Under the process conditions, the tensile strength of the 7050 alloy is 578MPa, the yield strength is 540MPa, and the elongation is 20.6%.
Example 4
Carrying out hot rolling deformation on the alloy at 460-480 ℃, wherein the reduction is 95%; heating the alloy at 465 ℃, preserving heat for 3 hours for solution treatment, and then quenching the alloy in water at 23 ℃ at room temperature, wherein the sample transfer time is required to be less than 5 seconds; immediately preserving the heat of the quenched alloy at 120 ℃ for 26 hours, performing pre-aging treatment, and cooling in water at the room temperature of 23 ℃ to ensure that the sample transfer time is less than 5 seconds. Heating the pre-aged alloy to 260 ℃ at a heating rate of 5 ℃ per minute, carrying out regression heating, and cooling in water at the room temperature of 26 ℃, wherein the sample transfer time is required to be less than 5 seconds; and (3) preserving the heat of the regressed alloy for 26 hours at the temperature of 125 ℃, performing re-aging treatment, and finally performing air cooling. Under the process conditions, the tensile strength of the 7050 alloy is 569MPa, the yield strength is 522MPa, and the elongation is 20%.
Comparative example 1
Carrying out hot rolling deformation on the alloy at 460-480 ℃, wherein the reduction is 95%; heating the alloy at 475 ℃, preserving heat for 1 hour to carry out solution treatment, and then quenching the alloy in water at 25 ℃ at room temperature, wherein the sample transfer time is less than 5 seconds; immediately preserving the heat of the quenched alloy for 24 hours at 120 ℃, performing pre-aging treatment, and cooling in water at 25 ℃ at room temperature, wherein the sample transfer time is required to be less than 5 seconds. Heating the pre-aged alloy to 300 ℃ at a heating rate of 5 ℃ per minute, performing regression heating, and cooling in water at room temperature of 25 ℃, wherein the sample transfer time is required to be less than 5 seconds; and (3) preserving the heat of the regressed alloy for 24 hours at the temperature of 120 ℃, performing re-aging treatment, and finally performing air cooling. Under the process conditions, the tensile strength of the 7050 alloy is 507MPa, the yield strength is 436MPa, and the elongation is 20.2%.
Comparative example 2
And (3) carrying out hot rolling deformation on the alloy at the temperature of 460-480 ℃, wherein the reduction is 95%. Under the process conditions, the tensile strength of the 7050 alloy is 327MPa, the yield strength is 299MPa, and the elongation is 9.6%.
Comparative example 3
The tensile strength of the commercial 7050 plate under the condition of T73651 is 510MPa, the yield strength is 455MPa, and the elongation is 11%.
TABLE 17050 comparison of mechanical Properties of alloys under different Process conditions
Claims (7)
1. A heat treatment method for synchronously improving the strength and the elongation of a 7-series aluminum alloy plate is characterized in that:
taking a 7050 aluminum alloy hot rolled plate as a treatment object, and sequentially adopting solid solution treatment, pre-aging treatment, regression heating treatment and re-aging treatment; obtaining a product;
the solid solution treatment comprises the following steps: preserving the heat for 1 to 3 hours at the temperature of 460 to 480 ℃, transferring the product into a cooling medium within 5 seconds, and quenching the product; the temperature of a cooling medium in the quenching process is 22-26 ℃;
the pre-aging treatment comprises the following steps: heating the plate subjected to the solution treatment to 115-130 ℃, preserving the temperature for 20-30 hours, transferring the plate into a cooling medium, and quenching; the temperature of a cooling medium in the quenching process is 22-26 ℃;
the regression heating treatment comprises the following steps: heating the pre-aged plate to a set temperature at a speed of 5 ℃/min, transferring the plate to a cooling medium within 5s, and cooling; the set temperature is 160-260 ℃;
the re-aging treatment comprises the following steps: heating the plate subjected to the returning heating treatment to 115-130 ℃, preserving heat, performing aging treatment for 20-30 hours, and cooling;
the preparation process of the 7050 aluminum alloy hot rolled plate comprises the following steps: heating 7050 aluminum alloy serving as a raw material, and then carrying out hot rolling, wherein the deformation of the hot rolling is more than or equal to 95%; the temperature is controlled to be 450-480 ℃ during hot rolling.
2. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 1, characterized in that: the thickness of the 7050 aluminum alloy hot-rolled plate is 1-3 mm.
3. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 1, characterized in that: the cooling medium includes water.
4. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 1, characterized in that; the set temperature is 180-.
5. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 4, characterized in that; the set temperature is 188-192 ℃; after reaching the set temperature, the mixture was transferred to water for cooling within 5 seconds.
6. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 1, characterized in that; when the aluminum alloy plate is a 7050 aluminum alloy plate, the tensile strength of the obtained product is 565-590 MPa, the yield strength is 520-560 MPa, and the elongation is 20-23.5%.
7. The heat treatment method for synchronously improving the strength and the elongation of the 7-series aluminum alloy plate according to claim 6, characterized in that; when the aluminum alloy plate is a 7050 aluminum alloy plate, the tensile strength of the obtained product is 575-590 MPa, the yield strength is 540-560 MPa, and the elongation is 20.5-23.5%.
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