CN112226636A - Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate - Google Patents

Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate Download PDF

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CN112226636A
CN112226636A CN202010935579.6A CN202010935579A CN112226636A CN 112226636 A CN112226636 A CN 112226636A CN 202010935579 A CN202010935579 A CN 202010935579A CN 112226636 A CN112226636 A CN 112226636A
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alloy
annealing
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余鑫祥
戴菡
赵志国
史丹丹
史先利
董晓燕
刘文文
李彩琼
赵俊凤
朱鹏程
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Yantai Nanshan University
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/03—Making non-ferrous alloys by melting using master alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C1/00—Making non-ferrous alloys
    • C22C1/02—Making non-ferrous alloys by melting
    • C22C1/026—Alloys based on aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/001—Aluminium or its alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/005—Copper or its alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/008—Zinc or its alloys

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  • Crystallography & Structural Chemistry (AREA)
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Abstract

The invention relates to a preparation method of a high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy, which utilizes the effective regulation and control effect of trace Ce addition on the microstructure of the Al-Zn-Mg-Cu-Zr alloy, ensures the alloy strength and improves the corrosion resistance of the alloy as much as possible. In addition, the heat treatment process of regression and re-aging is assisted, so that the problems that the Cu content of an alloy grain boundary precipitated phase is relatively low and the corrosion resistance of the alloy is influenced to a certain extent due to the addition of trace Ce are solved. The method specially utilized by the invention has no special condition requirement and mature process condition, thereby being particularly suitable for commercial large-scale production.

Description

Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate
Technical Field
The invention belongs to the field of non-ferrous metal alloy, and particularly relates to a preparation method of a high-strength and high-toughness corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate.
Background
The Al-Zn-Mg-Cu alloy has excellent specific strength and is widely applied to the field of aerospace. With the increasing demand of the engineering field for improving the strength of the alloy, the development of the alloy tends to be high alloyed and thereby promotes the volume fraction and the number density of precipitated phases in the alloy to be greatly improved. However, with the increase of the contents of main alloying elements Zn and Mg, the corrosion resistance of the alloy is greatly reduced, for example, higher strength is easily obtained in a T6 state peak aging state, but the corrosion performance is greatly weakened. Even though the corrosion resistance of the alloy can be greatly improved in the overaging annealing state of T7x, the alloy can sacrifice the strength value of 10-15%.
At present, extensive research is carried out on how to improve the high strength and good corrosion resistance of Al-Zn-Mg-Cu alloys. The method mainly improves the comprehensive strength and corrosion resistance of the alloy by disturbing the continuity of the grain boundary precipitated phase, increasing the distance of the grain boundary precipitated phase and simultaneously keeping the microstructure characteristics of fine dispersion distribution of the precipitated phase in the alloy crystal. Therefore, researchers develop heat treatment processes such as return re-aging (RRA), non-isothermal aging (NIA) and high-temperature pre-precipitation Heat Treatment (HTPP) to realize effective regulation and control of the microstructure of the alloy. Meanwhile, research shows that the inhibition of recrystallization is also beneficial to improving the corrosion resistance and the strength of the Al-Zn-Mg-Cu alloy, because the subgrain boundary of the alloy does not form an obvious precipitate-free precipitation zone (PFZ). In addition, the higher Cu content of the grain boundary phase is also beneficial to improving the corrosion resistance of the Al-Zn-Mg-Cu alloy. The alloying element Cu can reduce the electronegativity of a grain boundary phase, thereby influencing the anode polarization behavior of the alloy. However, there are currently few research techniques for comprehensively improving the strength and corrosion resistance of highly alloyed Al-Zn-Mg-Cu-Zr alloys through the synergistic effect of trace Ce and heat treatment.
In corrosive environment, Ce is added into the aluminum alloy to promote Al on the surface of the alloy2O3The corrosion resistance of the alloy is greatly improved by converting the film into an oxide film containing Ce, and the corrosion inhibition effect of the alloy is obviously better than that of La2O3、Nd2O3、Pr2O3、Y2O3And the like. And researches show that the addition of Ce can change the matrix precipitated phase in Al-Zn-Mg-Cu from spherical to needle-shaped, so that the tensile strength of the Al-Zn-Mg-Cu alloy is improved by 10 percent, and meanwhile, the recrystallization resistance of the Al-Cu-Li-Zr alloy is greatly improved due to the addition of Ce. It is worth noting that Ce is easy to interact with other elements in the alloy to form intermetallic compounds, so that the chemical composition of grain boundary precipitates is changed, and the performance of the alloy is further influenced. Therefore, the corrosion resistance and the strength of the alloy can be improved hopefully by adding trace Ce in the high-alloying Al-Zn-Mg-Cu alloy and assisting a proper heat treatment process.
Disclosure of Invention
In order to solve one of the technical problems or problems, the corrosion resistance (peeling corrosion and intergranular corrosion) and the mechanical property (strength and hardness) of the high-alloying Al-Zn-Mg-Cu are improved through the synergistic action of the addition of the Ce and the heat treatment, and the preparation of the high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy is realized. The Ce microalloying method has the advantages of obvious effect of improving the performance of structural materials, simple equipment requirement, easy operation, good controllability and good reproducibility, greatly reduces the cost compared with the traditional method, can be combined with the traditional heat treatment process, and is favorable for industrial production. Meanwhile, the comprehensive regulation and control of the alloy microstructure by Ce, such as the interruption and coarsening of a crystal boundary precipitated phase, the promotion of the Cu content and the improvement of the proportion of subcrystal boundaries, and the construction of an oxide film containing Ce on the alloy surface can be synchronously realized, so that the method has obvious advantages, and the development of the Al-Zn-Mg-Cu-Zr-Ce alloy is simple and efficient, and has practical application value as a potential high-performance structural material in the field of aerospace.
The invention adopts the following technical scheme:
a preparation method of a high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate comprises the following steps:
a. smelting and casting: smelting is carried out in a well-type resistance furnace by using a high-purity graphite crucible, wherein the raw materials comprise industrial pure Al, pure Mg, pure Zn and intermediate alloys Al-Cu, Al-Zr and Al-Ce, when the temperature is raised to 760-780 ℃ during smelting, the pure Al is added into the graphite crucible, the intermediate alloys Al-Cu, Al-Zr and Al-Ce are added for heating and melting, and a refining covering agent is spread on the surface of an alloy melt; after the alloy is melted, putting hexachloroethane into a bell jar and pressing the hexachloroethane into the melt, slagging off after degassing is finished, and spreading a refining covering agent for the second time; adding pure Zn into the crucible by using a clamp, adding Mg into the crucible by using a bell jar after the pure Zn is completely fused, standing for a period of time, performing secondary degassing and slagging off, and spreading a refining covering agent; standing for 5 minutes, then casting at the temperature of 710-740 ℃, wherein the casting is carried out by adopting an inclined die ingot casting and water-cooled copper die chilling technology, and argon protection and circulating cooling water are introduced in the whole casting process; the size of the finished cast ingot is 300 mm multiplied by 200 mm multiplied by 30 mm;
b. homogenizing and annealing: carrying out two-stage homogenizing annealing on the cast ingot in an air furnace, wherein the annealing is carried out for 6-10h at 435 +/-2 ℃ in the first step, the annealing is carried out for 20-40h at 470 +/-2 ℃ in the second step, and the temperature error is strictly controlled to +/-2 ℃;
c. plate forming: after the homogenization annealing, the cast ingot is firstly processed by head cutting, tail cutting and face milling
Hot rolling:
before hot rolling, the cast ingot is placed in an air annealing furnace at the temperature of 430 +/-5 ℃, the temperature is kept for 60-90min, and in the first step, the cast ingot is hot rolled to 20 +/-0.5 mm through 5 passes: the specific hot rolling thickness variation is as follows: 30 mm → 28 + -0.5 mm → 26 + -0.5 mm → 24 + -0.5 mm → 22 + -0.5 mm → 20 + -0.5 mm; re-melting and holding at 430 + -5 deg.C for 40-60min, and hot rolling to 5 + -0.5 mm in the second step by 5 passes: the specific hot rolling thickness variation is as follows: 20 +/-0.5 mm → 17 +/-0.5 mm → 14 +/-0.5 mm → 11 +/-0.5 mm → 8 +/-0.5 mm → 5 +/-0.5 mm;
cold rolling:
before cold rolling, the sheet is subjected to intermediate annealing at 430 +/-5 ℃ for about 1.5-2h, and is cooled to room temperature along with a furnace and taken out, wherein the specific cold rolling thickness of the alloy is changed as follows: 5 +/-0.5 mm → 4.8 +/-0.1 mm → 4.6 +/-0.1 mm → 4.4 +/-0.1 mm → 4.2 +/-0.1 mm → 4.0 +/-0.1 mm → 3.8 +/-0.1 mm → 3.6 +/-0.1 mm → 3.4 +/-0.1 mm → 3.2 +/-0.1 mm → 3.0 +/-0.1 mm → 2.8 +/-0.1 mm → 2.6 +/-0.1 mm → 2.4 +/-0.1 mm → 2.2 +/-0.1 mm, and obtaining the alloy cold-rolled plate.
d. Solution aging heat treatment: the method is carried out in a salt bath furnace capable of accurately controlling the temperature, the furnace temperature needs to be strictly controlled within the range of +/-2 ℃, the alloy plate is immediately quenched and cooled in a water tank when the solution time is up to the solid solution time, the water temperature is controlled below 25 ℃, and the quenching transfer time is less than 6 s; the alloy plates with different strength values and corrosion properties are obtained by respectively adopting the following aging heat treatment processes: if the peak value is aged at 120 ℃, artificially aging for 20-30h to obtain T6; overaging at 120 deg.C for 20-30h, and aging at 160 deg.C for 6-8h to obtain T7; treating at 120 deg.C for 20-30h, then performing regression annealing at 190 deg.C for 0.5-1h, and finally artificially aging at 120 deg.C for 20-30h to obtain RRA; the aging treatment is carried out in a blast drying oven with accurate temperature control, and the error is controlled to be +/-0.5.
Further, in the step a, a mixture of sodium chloride, potassium chloride and sodium fluoroaluminate in a ratio of 2:2:1 is used as a refining covering agent, the refining covering agent is always placed in a drying box for drying, the adding amount of the refining covering agent in the first two times is 6% of the total mass of the alloy, and the adding amount of the refining covering agent in the third time is 2% of the total mass of the alloy.
Further, in step a, the purity of the industrial pure Al is 99.87 wt%, the purity of the pure Mg is 99.92 wt%, the purity of the pure Zn is 99.94 wt%, the purity of the intermediate alloy Al-Cu is 51.51 wt%, the purity of the intermediate alloy Al-Zr is 3.29 wt%, and the purity of the intermediate alloy Al-Ce is 10.01 wt%.
Further, in the step a, the raw materials comprise the following components in parts by mass: 7.10-9.50Zn, 1.85-2.15Mg, 2.05-2.45Cu, 0.10-0.11Zr, 0.02-0.08Fe, 0.02-0.05Si and 0.05-0.25 Ce.
Further, in the step c, before the hot rolling is started, a liquefied gas flame thrower is adopted to preheat the roller of the rolling mill to 90-100 ℃, the low-speed rolling at 400r/min is adopted in the cogging hot rolling stages from the 1 st pass to the 5 th pass, and the high-speed rolling at 900r/min is adopted in the 5-pass hot rolling.
Further, in the step d, the solution treatment is secondary solution treatment, the solution treatment is carried out for 40-60min at 450 +/-2 ℃, and then the solution treatment is carried out for 20-40min at 485 +/-2 ℃.
The invention has the following beneficial technical effects: the invention utilizes the effective regulation and control effect of trace Ce addition on the microstructure of the Al-Zn-Mg-Cu-Zr alloy, such as inhibiting recrystallization to improve the proportion of subboundary in the alloy, continuously changing the crystal boundary precipitated phase of the T6 alloy into discontinuous phase, and promoting the formation of a Ce oxide film with the strongest rare earth corrosion inhibition effect on the surface of the alloy, thereby ensuring the strength of the alloy and improving the corrosion resistance of the alloy as much as possible. In addition, the heat treatment process of regression and re-aging is assisted, so that the problem that the Cu content of an alloy grain boundary precipitated phase is relatively low due to addition of trace Ce, and certain negative influence is caused on the corrosion resistance of the alloy grain boundary precipitated phase is solved. The method provides a new effective technical means for the high-strength corrosion-resistant aerospace Al-Zn-Mg-Cu structural material, and provides a new idea for the development and industrial application of the related high-comprehensive-performance aluminum alloy structural material. The microalloying and conventional heat treatment methods have the advantages of simple equipment requirement, easy operation, large range, good controllability and good reproducibility, and the cost is greatly reduced compared with the conventional method. The method specially utilized by the invention has no special condition requirement and mature process condition, thereby being particularly suitable for commercial large-scale production.
Detailed Description
a. Smelting and casting: alloy melting was carried out in a well-type resistance furnace using a high-purity graphite crucible. The mixture of sodium chloride, potassium chloride and sodium fluoroaluminate (mixed in a ratio of 2:2: 1) is used as a refining covering agent and spread on the surface of the alloy melt for smelting, so that moist air is isolated, hydrogen absorption of the melt is prevented, and the mixture is also used as a refining agent to improve the alloy smelting effect. When smelting, industrial pure Al (99.87 wt%), pure Mg (99.92 wt%), pure Zn (99.94 wt%), andthe master alloy Al-Cu (51.51 wt%), Al-Zr (3.29 wt%) and Al-Ce (10.01 wt%) as raw materials. When the temperature is raised to 760 ℃, pure Al is added into the graphite crucible, Al-Cu, Al-Zr and Al-Ce intermediate alloys are added at the same time for heating and melting, and refining covering agent with the total mass of 6 percent of the alloy is added (the covering agent is always placed in a drying oven for drying). After the alloy is melted, hexachloroethane (C) is used2Cl6) Placing the alloy in a bell jar, pressing the alloy into the melt, removing slag after degassing, and adding a refining covering agent accounting for 6 percent of the total mass of the alloy for the second time. And then adding pure Zn into the crucible by using a clamp, adding Mg into the crucible by using a bell jar after the pure Zn is completely fused, standing for a period of time, then performing secondary degassing and slagging off, and simultaneously adding a refining covering agent accounting for 2% of the total mass of the alloy. After standing for 5 minutes, casting was carried out at a temperature of 720 ℃. The casting is carried out by adopting an inclined die ingot casting and water-cooling copper die chilling technology, and argon protection and circulating cooling water are introduced in the whole casting process. The size of the finished ingot is about 300 mm multiplied by 200 mm multiplied by 30 mm. The alloy comprises the following components in percentage by mass: 8.75Zn, 2.05Mg, 2.22Cu, 0.11Zr, 0.05Fe, 0.03Si, 0.12Ce and the balance of Al.
b. Homogenizing and annealing: before experimental homogenization annealing, samples of the top and bottom regions of an alloy ingot are intercepted, and the secondary homogenization upper limit temperatures of the alloy are respectively 440 ℃ and 475 ℃ determined by adopting an experimental result of differential thermal analysis (DSC). Homogenizing and annealing the ingot in an air furnace, and strictly controlling the temperature error to be +/-2 ℃. The invention adopts a two-stage homogenization annealing process, namely, the first step of annealing at 435 +/-2 ℃ for 8 hours, and the second step of annealing at 470 +/-2 ℃ for 32 hours.
c. Plate forming: and after homogenizing annealing, performing head and tail cutting and face milling treatment on the alloy. Before hot rolling, the aluminum ingot is placed in an air annealing furnace at the temperature of 430 +/-5 ℃ and is kept for 60 min. Before hot rolling begins, a roller of a rolling mill is preheated to 90-100 ℃ by a liquefied gas flame thrower, and the roller is hot rolled to 20 +/-0.5 mm (the rotating speed of the rolling mill is 300r/min) in a first step by 5 passes. The specific hot rolling thickness variation is as follows: 30 mm → 28. + -. 0.5mm → 26. + -. 0.5mm → 24. + -. 0.5mm → 22. + -. 0.5mm → 20. + -. 0.5 mm. The furnace is re-melted and kept at the temperature of 430 +/-5 ℃ for 50min, and then the second step is hot rolled to 5 +/-0.5 mm (the rotating speed of the rolling mill is 700r/min) by 5 passes. The specific hot rolling thickness variation is as follows: 20 + -0.5 mm → 17 + -0.5 mm → 14 + -0.5 mm → 11 + -0.5 mm → 8 + -0.5 mm → 5 + -0.5 mm. Before cold rolling, the plate is subjected to intermediate annealing at 430 +/-5 ℃ for about 1.5h, and is cooled to room temperature along with a furnace and taken out. The specific cold rolling process of the alloy comprises the following steps: 5.0 mm → 4.8. + -. 0.1 mm → 4.6. + -. 0.1 mm → 4.4. + -. 0.1 mm → 4.2. + -. 0.1 mm → 4.0. + -. 0.1 mm → 3.8. + -. 0.1 mm → 3.6. + -. 0.1 mm → 3.4. + -. 0.1 mm → 3.2. + -. 0.1 mm → 3.0. + -. 0.1 mm → 2.8. + -. 0.1 mm → 2.6. + -. 0.1 mm → 2.4. + -. 0.1 mm → 2.2. + -. 0.1 mm.
d. Solution aging heat treatment: the solution treatment is carried out in a salt bath furnace capable of accurately controlling the temperature (solution treatment is carried out for 50min at 450 +/-2 ℃ and then for 30 min at 485 +/-2 ℃), the alloy plate is immediately quenched and cooled in a water tank when the solution time is up to the point, the water temperature is controlled below 25 ℃, and the quenching transfer time is less than 6 s. The alloy plates with different strength values and corrosion properties are obtained by respectively adopting the following aging heat treatment processes: for example, peak ageing at 120 ℃ for 24h (T6), overaging at 120 ℃ for 24h, and subsequent high temperature ageing at 160 ℃ for 8h (T7). Treating at 120 deg.C for 24h, then performing regression annealing at 190 deg.C for 0.5h, and finally artificially aging at 120 deg.C for 24h (RRA). The aging treatment of the test alloy is carried out in a forced air drying oven with accurate temperature control, and the error is controlled to be +/-0.5.

Claims (6)

1. A preparation method of a high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate is characterized by comprising the following steps:
a. smelting and casting: smelting is carried out in a well-type resistance furnace by using a high-purity graphite crucible, wherein the raw materials comprise industrial pure Al, pure Mg, pure Zn and intermediate alloys Al-Cu, Al-Zr and Al-Ce, when the temperature is raised to 760-780 ℃ during smelting, the pure Al is added into the graphite crucible, the intermediate alloys Al-Cu, Al-Zr and Al-Ce are added for heating and melting, and a refining covering agent is spread on the surface of an alloy melt; after the alloy is melted, putting hexachloroethane into a bell jar and pressing the hexachloroethane into the melt, slagging off after degassing is finished, and spreading a refining covering agent for the second time; adding pure Zn into the crucible by using a clamp, adding Mg into the crucible by using a bell jar after the pure Zn is completely fused, standing for a period of time, performing secondary degassing and slagging off, and spreading a refining covering agent; standing for 5 minutes, then casting at the temperature of 710-740 ℃, wherein the casting is carried out by adopting an inclined die ingot casting and water-cooled copper die chilling technology, and argon protection and circulating cooling water are introduced in the whole casting process; the size of the finished cast ingot is 300 mm multiplied by 200 mm multiplied by 30 mm;
b. homogenizing and annealing: carrying out two-stage homogenizing annealing on the cast ingot in an air furnace, wherein the annealing is carried out for 6-10h at 435 +/-2 ℃ in the first step, the annealing is carried out for 20-40h at 470 +/-2 ℃ in the second step, and the temperature error is strictly controlled to +/-2 ℃;
c. plate forming: after the homogenization annealing, the cast ingot is firstly processed by head and tail cutting and face milling,
hot rolling:
before hot rolling, the cast ingot is placed in an air annealing furnace at the temperature of 430 +/-5 ℃, the temperature is kept for 60-90min, and in the first step, the cast ingot is hot rolled to 20 +/-0.5 mm through 5 passes: the specific hot rolling thickness variation is as follows: 30 mm → 28 + -0.5 mm → 26 + -0.5 mm → 24 + -0.5 mm → 22 + -0.5 mm → 20 + -0.5 mm; re-melting and holding at 430 + -5 deg.C for 40-60min, and hot rolling to 5 + -0.5 mm in the second step by 5 passes: the specific hot rolling thickness variation is as follows: 20 +/-0.5 mm → 17 +/-0.5 mm → 14 +/-0.5 mm → 11 +/-0.5 mm → 8 +/-0.5 mm → 5 +/-0.5 mm;
cold rolling:
before cold rolling, the sheet is subjected to intermediate annealing at 430 +/-5 ℃ for about 1.5-2h, and is cooled to room temperature along with a furnace and taken out, wherein the specific cold rolling thickness of the alloy is changed as follows: 5 +/-0.5 mm → 4.8 +/-0.1 mm → 4.6 +/-0.1 mm → 4.4 +/-0.1 mm → 4.2 +/-0.1 mm → 4.0 +/-0.1 mm → 3.8 +/-0.1 mm → 3.6 +/-0.1 mm → 3.4 +/-0.1 mm → 3.2 +/-0.1 mm → 3.0 +/-0.1 mm → 2.8 +/-0.1 mm → 2.6 +/-0.1 mm → 2.4 +/-0.1 mm → 2.2 +/-0.1 mm, to obtain the alloy cold-rolled plate;
d. solution aging heat treatment: the method is carried out in a salt bath furnace capable of accurately controlling the temperature, the furnace temperature needs to be strictly controlled within the range of +/-2 ℃, the alloy plate is immediately quenched and cooled in a water tank when the solution time is up to the solid solution time, the water temperature is controlled below 25 ℃, and the quenching transfer time is less than 6 s; the alloy plates with different strength values and corrosion properties are obtained by respectively adopting the following aging heat treatment processes: if the peak value is aged at 120 ℃, artificially aging for 20-30h to obtain T6; overaging at 120 deg.C for 20-30h, and aging at 160 deg.C for 6-8h to obtain T7; treating at 120 deg.C for 20-30h, then performing regression annealing at 190 deg.C for 0.5-1h, and finally artificially aging at 120 deg.C for 20-30h to obtain RRA; the aging treatment is carried out in a blast drying oven with accurate temperature control, and the error is controlled to be +/-0.5.
2. The method for preparing Al-Zn-Mg-Cu-Zr-Ce alloy plate with high strength and corrosion resistance as claimed in claim 1, wherein in step a, a mixture of sodium chloride, potassium chloride and sodium fluoroaluminate in a ratio of 2:2:1 is used as a refining covering agent, the refining covering agent is always placed in a drying oven for drying, the addition amount of the refining covering agent in the first two times is 6% of the total mass of the alloy, and the addition amount of the refining covering agent in the third time is 2% of the total mass of the alloy.
3. The method for preparing a high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate as claimed in claim 1, wherein in the step a, the purity of industrial pure Al is 99.87 wt%, the purity of pure Mg is 99.92 wt%, the purity of pure Zn is 99.94 wt%, the purity of intermediate alloy Al-Cu is 51.51 wt%, the purity of intermediate alloy Al-Zr is 3.29 wt%, and the purity of intermediate alloy Al-Ce is 10.01 wt%.
4. The preparation method of the high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate as claimed in claim 1, wherein in the step a, the mass percentages of the components are as follows: 7.10-9.50Zn, 1.85-2.15Mg, 2.05-2.45Cu, 0.10-0.11Zr, 0.02-0.08Fe, 0.02-0.05Si, 0.05-0.25Ce and the balance of Al.
5. The method as claimed in claim 1, wherein in step c, a liquefied gas burner is used to preheat the mill roll to 90-100 ℃ before the hot rolling, the low-speed rolling at 200-.
6. The method for preparing the Al-Zn-Mg-Cu-Zr-Ce alloy plate with high strength and corrosion resistance as claimed in claim 1, wherein in the step d, the solution treatment is secondary solution treatment, the solution treatment is carried out for 40-60min at 450 +/-2 ℃ and then for 20-40min at 485 +/-2 ℃.
CN202010935579.6A 2020-09-08 2020-09-08 Preparation method of high-strength corrosion-resistant Al-Zn-Mg-Cu-Zr-Ce alloy plate Pending CN112226636A (en)

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CN107119216A (en) * 2017-06-27 2017-09-01 中南大学 A kind of high-strength corrosion-resistant erosion aluminium alloy and preparation method thereof
CN108823472A (en) * 2018-07-25 2018-11-16 江苏大学 A kind of High Strength and Tenacity Al-Zn-Mg-Cu Aluminum Alloy and its heat treatment method

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US20050072497A1 (en) * 2002-04-05 2005-04-07 Frank Eberl Al-Zn-Mg-Cu alloys and products with high mechanical characteristics and structural members suitable for aeronautical construction made thereof
CN107119216A (en) * 2017-06-27 2017-09-01 中南大学 A kind of high-strength corrosion-resistant erosion aluminium alloy and preparation method thereof
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CN115261687A (en) * 2022-06-15 2022-11-01 烟台南山学院 High-alloying Al-Zn-Mg-Cu alloy and method for eliminating high-temperature-resistant residual phase
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Application publication date: 20210115