CN115125422B - Corrosion-resistant high-strength-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof - Google Patents
Corrosion-resistant high-strength-toughness Al-Li-Cu-Zr-Er alloy plate and preparation method thereof Download PDFInfo
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- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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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
- C22C1/026—Alloys based on aluminium
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- 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
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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
Abstract
The application discloses a corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate and a preparation method thereof. The chemical components of the alloy are optimized, the Cu content is reduced as much as possible while the alloy strength is ensured, the full precipitation of the main strengthening phase T1 is ensured, the tendency of weakening the grain boundary caused by the segregation of Li element in the grain boundary is reduced due to the low Li addition, and the corrosion resistance and the toughness of the alloy are improved. Through Er and Zr composite microalloying addition and low-temperature homogenization heat treatment process, nano-sized high-temperature stable phase Al with tiny dispersion distribution is constructed in the alloy 3 (Er, zr) particles, on the one hand, give play to Al 3 The (Er, zr) particles have stronger pinning effect on grain boundary migration, improve the capability of inhibiting recrystallization when the alloy is in solid solution at high temperature, and obtain fine fibrous sub-crystal structure (fine crystal strengthening), wherein the structure is beneficial to PFZ narrowing and grain boundary phase interruption; at the same time, a large amount of dispersed Al 3 The (Er, zr) particles lead to additional improvement in strength of the alloy.
Description
Technical Field
The application relates to the technical field of nonferrous metal alloys, in particular to a corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate and a preparation method thereof.
Background
The Al-Li-Cu alloy has the advantages of low density, high specific strength and specific stiffness, is always concerned by the aviation manufacturing industry, is considered to be an ideal light structural material of an aerospace vehicle in the 21 st century, and has great application potential in marine military equipment. The Chinese patent document CN11004328B discloses an Al-Li alloy added with 1.5-2% of Li,0.5-3.0% of Zn,0.1-0.3% of Cr,0.1-0.3% of Zr,0.1-0.3% of Yb and the balance of Al, and the Al-Li alloy is soaked in 3.5% wt. of NaCl solution for 72 hours, the inter-crystal corrosion depth is less than 100m, and the inter-crystal corrosion grade reaches 3 grades. The application removes Cu element in the alloy composition design, thereby eliminating a copper-rich area which is easy to generate anodic dissolution and helping the corrosion performance of the aluminum-lithium alloy to a certain extent. But also directly results in T1 (Al) 2 CuLi) phase is not existed, the alloy is difficult to obtain higher strength, and the application of the alloy as engineering components in marine military equipment is greatly limited. Chinese patent document CN 114075630A discloses a high-strength corrosion-resistant aluminum-lithium alloy plate and a preparation method thereof, wherein the high-strength corrosion-resistant aluminum-lithium alloy plate is added with 1.0-1.6 percent of Li,3.9-5.2 percent of Cu,0.4-0.7 percent of Mg,0.3-0.6 percent of Ag,0.1-0.3 percent of Cr,0.15-0.4 percent of Mn,0.1-0.3 percent of Ti and the balance of Al and impurities. The alloy plate has room temperature tensile strength exceeding 600Mpa after casting, two-stage homogenization, rolling, two-stage solution treatment and aging treatment, but the corrosion performance among the alloy is not evaluated, and particularly, the ultrahigh copper content (more than 3.9%) in the alloy causes a large amount of copper-containing phases with negative potential to be separated out from the alloy, so that the corrosion resistance of the alloy is possibly reduced. If researches show that the maximum inter-crystal corrosion depth of the Al-1.0Li-4.0Cu-0.4 Mg-0.4 Ag-0.14Zr (mass percent) wrought aluminum alloy reaches 340um, and the inter-crystal corrosion grade is as high as 5 grades. The method shows that the high copper alloying in the aluminum-lithium alloy can not be ignored for the harm to the corrosion resistance. In addition, as the comprehensive performance requirements of marine military equipment structural parts such as underwater missile launching platforms, anti-warships, torpedoes, deepwater bombs and the like are increasingly improved, the corrosion resistance is improved, and meanwhile, the toughness is also considered, butThere are few reports on this aspect.
In view of the above, the application develops the corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate. Can be used as a material required by novel marine military equipment structural members.
Disclosure of Invention
In order to solve the technical problems or one of the technical problems, the application aims to provide an optimized alloy chemical composition, reduce the copper content while ensuring the alloy strength, weaken the harmful influence brought by a copper-rich area which is easy to be dissolved by an anode, realize fine grain strengthening through the improvement of other components, and finally improve the corrosion resistance and the toughness of the alloy.
In order to achieve the effects, the application discloses a corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate which comprises the following components in percentage by mass:
li:0.6% -0.9%, 3.0% -3.8% of Cu, 0.2% -0.3% of Ag, 0.2% -0.3% of Mg, 0.25% -0.35% of Zr, 0.25% -0.35% of Er, 0.25% -0.03% of Fe, 0.01% -0.02% of Si and the balance of Al, wherein the mass ratio of Cu to Li is more than 4.
The Cu/Li ratio is ensured to be more than 4, meanwhile, the Cu content (less than 3.8 wt%) is reduced as much as possible, the whole process of the Er and Zr composite microalloying addition and preparation process is optimally controlled, the corrosion resistance, strength and toughness of the Al-Li-Cu alloy are improved, and the preparation of the corrosion-resistant high-toughness Al-Li-Cu-Zr-Er alloy plate is realized.
The application also discloses a preparation method of the corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which comprises the following steps:
a) Smelting and casting: alloy smelting is carried out in a resistance wire furnace, pure Al, pure Ag and intermediate alloys Al-Cu, al-Zr and Al-Er are put into a high-purity graphite crucible, a refining covering agent is added for the first time, and the temperature is raised to 780+/-10 ℃ along with the furnace; keeping the temperature for 5-10min, and adopting a proper amount of hexachloroethane (C) 2 Cl 6 ) Pressing the mixture into a melt in a bell jar, removing slag after degassing, and adding a proper amount of refining covering agent for the second time; then stabilizing the furnace temperature to about 740 ℃, adding Mg by using a bell jar, lifting the bell jar after the Mg is completely melted, stabilizing the furnace temperature to about 730 ℃, and finally, aluminum foil is usedPressing the vacuum packed pure Li into the melt by using a bell jar, and lifting the bell jar after the Li is completely melted; standing for 2min, performing secondary degassing and slag skimming, and adding a refining covering agent for the third time; standing for 5min, removing the cover layer on the surface with a ladle, and casting at 710 deg.C; the size of the finished cast ingot ranges from 100X 24mm to 300X 24mm;
b) Homogenizing annealing: homogenizing annealing the cast ingot in a vacuum atmosphere furnace, wherein the temperature error is strictly controlled to be +/-2 ℃; the application adopts a two-stage homogenizing annealing process, namely, the first stage is annealed for 8-10h at 410+/-10 ℃ and the second stage is annealed for 14-18h at 510-515+/-2 ℃;
c) Rolling the plate: the alloy plate is prepared by hot rolling, intermediate annealing and cold rolling;
d) Solid solution aging heat treatment: the solid solution is carried out in a salt bath furnace, and the aging treatment adopts single-stage aging and is carried out in a blast drying oven.
Further, in step a, the experimental raw materials had chemical compositions of pure Al 99.99 wt%, pure Mg 99.99%, pure Li 99.9%, ag 99.99%, and intermediate alloys Al-Cu 50.0%, al-Er 20.0 wt% and Al-Zr 10.0 wt%.
Further, in step a, the first addition of the refined covering agent is 8-10g, and the second and third additions are about 3-4g (i.e., used as covering agent only); the refining covering agent is formed by mixing LiF and LiCl in a ratio of 1:2 (the refining covering agent is always dried in a drying oven at 120 ℃); degassing agent hexachloroethane (C) 2 Cl 6 ) The addition amount of each time is 6-8g.
Furthermore, in the step a, a water-cooling copper mold is adopted as a crystallizer during casting, and the mold is rapidly cooled by argon protection and circulating cooling water during the whole casting process.
In the step b, the vacuum atmosphere furnace is vacuumized to 20-30Pa, and then nitrogen is introduced. In step b, the primary low-temperature homogenizing annealing aims at promoting the fine dispersion distribution of Al 3 (Er, zr) particles are fully separated out, so that preparation is made for high-temperature homogenization heat treatment, and overburning is prevented; the purpose of the second-stage high-temperature homogenizing annealing is to sufficiently eliminate unbalanced solidification phase and improve alloyingUniformity of the chemical composition.
In step c, the homogenized alloy is subjected to end cutting and surface milling before rolling, the upper and lower large surfaces are thinned by more than 1.5mm respectively, and if exposed point-shaped air holes are formed on the surface, the surface is cleaned by an angle grinder (the adverse effect of oxide impurities on the air hole wall on the mechanical properties of the alloy is eliminated).
Further, in the step c, before hot rolling starts, placing an ingot in an annealing furnace, preserving heat for 2-3 hours at the temperature of 450+/-10 ℃, and preheating a rolling mill roller to 120-180 ℃ by adopting a liquefied gas sprayer; in the step c, the total deformation of the hot rolling is not less than 75 percent, and the total deformation of the cold rolling is not less than 45 percent; in the step c, the sheet is subjected to intermediate annealing at 450+/-10 ℃ for about 1.5-2.5 h before cold rolling, and is cooled to room temperature along with a furnace and taken out.
In the step d, the solid solution temperature is 520+/-1 ℃, and the alloy plate is immediately quenched and cooled in a water tank after being subjected to solid solution for 50-70 min. The T86 sample needs to be subjected to cold rolling and pre-deformation before aging, the deformation is about 6%, the aging is carried out at 150 ℃, and the aging time is 12 h-20 hours;
in the step d, the water temperature of the quenching water tank is controlled to be about 25 ℃, and the quenching transfer time is less than 5s.
Advantageous results of the application
(1) Optimizing the chemical components of the alloy, ensuring the strength of the alloy (high Cu/Li ratio design, more than 4), reducing the Cu content as much as possible (not more than 3.8 wt%) and ensuring the main strengthening phase T1 (Al) 2 CuLi) phase is fully separated out, the tendency of weakening of a grain boundary caused by segregation of Li element at the grain boundary is reduced by low addition of Li, the harmful influence caused by a copper-rich area which is easy to dissolve in an anode is weakened to a certain extent by low addition of Cu, and the corrosion resistance and the toughness of the alloy are improved.
(2) According to the hierarchical relationship formed by the difference of diffusion coefficients of two elements of Er and Zr and the difference of nucleation capability, through Er and Zr composite microalloying addition and low-temperature homogenization heat treatment process, a nano-sized high-temperature stable phase Al with fine dispersion distribution is constructed in the alloy 3 (Er, zr) particles, on the one hand, give play to Al 3 (Er, zr) grainsThe seed has stronger pinning effect on grain boundary migration, improves the capability of inhibiting recrystallization when the alloy is in high-temperature solid solution, and obtains a fine fibrous subgrain structure (fine grain strengthening), and the structure is favorable for PFZ narrowing and grain boundary phase interruption; at the same time, a large amount of dispersed Al 3 The (Er, zr) particles lead to additional improvement of the strength (dispersion strengthening) of the alloy.
Therefore, the synergistic effect of the microalloy and the heat treatment leads to the grain refinement of the alloy, the increase of the number of small-angle grain boundaries, the narrowing of PFZ, the intermittent grain boundary phase and the weakening of the Li segregation of the grain boundary, and the comprehensive improvement of the corrosion resistance and the toughness of the alloy. The method has the advantages of simple equipment requirement, strong repeatability and suitability for large-scale commercial production, and has obvious advantages. Therefore, the Al-Li-Cu-Zr-Er alloy plate with corrosion resistance and high strength and toughness is developed, and has practical application value as a novel marine military equipment structural member material.
Drawings
FIG. 1 shows that a large amount of dispersed phase particles Al are precipitated in the homogenization process of the Al-Li-Cu-Zr-Er alloy 3 (Er,Zr)；
FIG. 2 shows the grain structure after solution treatment of Al-Li-Cu-Zr-Er alloy;
FIG. 3 shows the grain structure after solution treatment of Al-Li-Cu alloy;
FIG. 4 is a graph showing the distribution of grain boundary orientation differences in the grain structure after solution treatment of an Al-Li-Cu-Zr-Er alloy;
FIG. 5 is a grain boundary orientation difference distribution in a grain structure of an Al-Li-Cu alloy after solution treatment;
FIG. 6 shows the depth of intergranular corrosion attack after T8-state aging of Al-Li-Cu-Zr-Er alloys;
FIG. 7 shows the depth of intergranular corrosion attack after T8-state aging of Al-Li-Cu alloys;
FIG. 8 is a view of the microstructure of the grain boundary after T8-state aging treatment of the Al-Li-Cu-Zr-Er alloy;
FIG. 9 is a view of the microstructure of the grain boundary after T8 aging treatment of the Al-Li-Cu alloy;
FIG. 10 is a graph showing tensile properties and fracture toughness of an alloy of the present application.
Detailed Description
The application will be further described with reference to the accompanying drawings and specific embodiments. It is to be understood that these examples are illustrative of the present application and are not intended to limit the scope of the present application. Further, it will be understood that various changes and modifications may be made by those skilled in the art after reading the teachings of the application, and equivalents thereof fall within the scope of the application as defined by the claims. Hereinafter, wt% is mass%.
Examples:
a preparation method of a corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate comprises the following steps:
a) Smelting and casting: alloy smelting is carried out in a resistance wire furnace, pure Al, pure Ag and intermediate alloys Al-Cu, al-Zr and Al-Er are put into a high-purity graphite crucible, 8g of refining covering agent (LiF and LiCl are mixed in a ratio of 1:2, and the refining covering agent is always placed in a drying box at 120 ℃ for drying) is added for the first time, and each raw material is adopted: pure Al (99.99 wt%), ag (99.99 wt%), and the master alloys Al-Cu (50.0 wt%), al-Er (20.0 wt%), al-Zr (10.0 wt%).
The raw materials are heated to 780+/-10 ℃ along with the furnace. After the raw materials are completely melted after the temperature is kept for 6min, 6g of hexachloroethane (C 2 Cl 6 ) Placing the mixture into a bell jar, pressing the mixture into a melt, removing slag after degassing, and adding 3g of refining covering agent for the second time. Then the furnace temperature is stabilized at about 740 ℃, mg is added by a bell jar, and the bell jar is provided after the Mg is completely melted, wherein the Mg raw material adopts pure Mg (99.99 wt%).
The furnace temperature is stabilized at about 730 ℃, pure Li packed in vacuum and wrapped by aluminum foil is pressed into melt by a bell jar, and the bell jar is put out after Li is completely melted. And standing for 2min, performing secondary degassing and slag skimming, and adding 3g of refining covering agent for the third time. After standing for 5min, the coating on the surface is scraped off by an iron ladle, and the temperature is stabilized at about 710 ℃ for casting. The crystallizer adopts a water-cooling copper mold during casting, and argon is introduced in the whole casting process to protect and circulate cooling water to rapidly cool the mold. The size range of the finished cast ingot is 100×100 mm ×24mm. Wherein, the Li raw material adopts pure Li (99.9 wt percent) and the like.
b. Homogenizing and annealing: homogenizing the cast ingot in a vacuum atmosphere furnaceAnnealing, wherein the temperature error is strictly controlled at +/-2 ℃, vacuumizing in a vacuum atmosphere furnace until the pressure is 20-30Pa, and then introducing nitrogen. The application adopts a two-stage homogenizing annealing process, namely, the first stage is annealed for 8 hours at 410 ℃, and the second stage is annealed for 16 hours at 510+/-2 ℃. The purpose of the primary low-temperature homogenizing annealing is to promote the fine dispersion distribution of Al 3 (Er, zr) particles are fully precipitated (figure 1), so that preparation is made for high-temperature homogenization heat treatment, and over-burning is prevented; the purpose of the second-stage high-temperature homogenizing annealing is to sufficiently eliminate unbalanced solidification phase and improve the uniformity of chemical components of the alloy.
And (3) performing end-cutting and surface milling treatment on the alloy ingot after the homogenization annealing, wherein the thickness of the ingot is controlled to be about 21mm when the upper and lower large surfaces are thinned by 1.5mm respectively and an angle grinder is used for cleaning up the exposed point-shaped air holes on the surfaces (eliminating adverse effects on the mechanical properties of the alloy caused by oxide impurities on the air hole walls).
c. And (3) rolling a plate: before hot rolling starts, a rolling mill roller is preheated to 120-180 ℃ by adopting a liquefied gas sprayer, meanwhile, an ingot casting is placed in an annealing furnace for heat preservation for 2 hours at the temperature of 450+/-10 ℃, then hot rolling is carried out for multiple passes from 21mm to 4.4mm, the total deformation of the hot rolling is 79.05%, the sheet is subjected to intermediate annealing for about 1.5 h at the temperature of 450+/-10 ℃ before cold rolling, and is taken out after being cooled to room temperature, then hot rolling is carried out for multiple passes from 4.4mm to 2.2mm, and the total deformation of the cold rolling is 50.00%.
d. And (3) solid solution aging heat treatment: the solid solution is carried out in a salt bath furnace, the solid solution temperature is 520+/-1 ℃, the alloy plate is immediately quenched and cooled in a water tank after the solid solution is carried out for 50min, the water temperature of the quenching water tank is controlled to be about 25 ℃, and the quenching transfer time is less than 5s. The aging treatment adopts single-stage aging and is carried out in a blast drying oven. The T86 sample was subjected to cold rolling and pre-deformation before aging, the deformation amount was about 6%, and the aging time was 15 h at 150 ℃.
Finally, the cold-rolled sheet is obtained by the following elements in percentage by mass:
li: 0.8%, cu 3.4%, ag 0.2%, mg 0.2%, zr 0.3%, er 0.3%, fe 0.03%, si 0.02% and the balance of Al.
Comparative example:
preparation of a common Al-Li-Cu alloy Li was prepared according to the conventional method: 0.8%, cu 3.6%, ag 0.2%, mg 0.2%, fe 0.03%, si 0.02% and the balance of Al.
After the preparation of the alloy plate is finished, microscopic analysis and performance detection are carried out on the product:
(1) The microstructure of the alloy cold-rolled sheet after solution treatment is observed and studied by adopting metallography and EBSD microstructure is shown in figures 2 to 5. Obviously, after annealing at 520 ℃ for 50min, compared with the base alloy which is completely recrystallized and the large-angle grain boundary is relatively high, the alloy added with Er and Zr by compounding also maintains deformed fiber tissue and the small-angle grain boundary volume fraction is relatively high, so that the newly designed alloy containing Er and Zr is refined and the number of small-angle grain boundaries is increased.
(2) As shown in the experimental results of the inter-crystal corrosion test of GB/T7998-2005, compared with the base alloy of the comparative example, the inter-crystal corrosion depth of the alloy with the Er and Zr added in a composite way is reduced from 273.48m to 60.48m, and the inter-crystal corrosion grade is reduced from 4 grade to 3 grade. The reason is that the corrosion resistance of the alloy is improved due to the grain refinement of the newly designed alloy and the increase in the number of small angle grain boundaries, PFZ narrowing, and the increase in the dispersion of the grain boundary equilibrium phase (fig. 8 and fig. 9).
(3) The tensile properties and fracture toughness properties of the Er and Zr added alloy and the base alloy are compared by adopting a normal temperature tensile property test and a Kahn tearing experiment method, and the tensile properties and fracture toughness properties of the Er and Zr added alloy and the base alloy are shown in figure 10. The results show that the newly designed Al-Li-Cu-Zr-Er alloy has fine grain structure (fine grain strengthening) and a large amount of Al with strong combination with the matrix 3 The precipitation (dispersion strengthening) of the (Er, zr) nano particles leads to the comprehensive improvement of the strength, the shaping and the fracture toughness.
The above examples are only illustrative of the preferred embodiments of the present application and do not limit the scope of the present application, and various modifications and improvements made by those skilled in the art to the technical solution of the present application should fall within the protection scope defined by the claims of the present application.
Claims (9)
1. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate is characterized by comprising the following components in percentage by mass: li:0.6% -0.9%, 3.0% -3.8% of Cu, 0.2% -0.3% of Ag, 0.2% -0.3% of Mg, 0.25% -0.35% of Zr, 0.25% -0.35% of Er, 0.25% -0.03% of Fe, 0.01% -0.02% of Si and the balance of Al, wherein the mass ratio of Cu to Li is more than 4; the corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate is obtained through the following steps:
a) Smelting and casting: alloy smelting is carried out in a resistance wire furnace, pure Al, pure Ag and intermediate alloys Al-Cu, al-Zr and Al-Er are put into a high-purity graphite crucible, a refining covering agent is added for the first time, and the temperature is raised to 780+/-10 ℃ along with the furnace; keeping the temperature for 5-10min, after the raw materials are completely melted, placing a proper amount of hexachloroethane into a bell jar to be pressed into the melt, slagging off after degassing is finished, and adding a proper amount of refining covering agent for the second time; then, the furnace temperature is stabilized at about 740 ℃, mg is added by a bell jar, the bell jar is put out after the Mg is completely melted, the furnace temperature is stabilized at about 730 ℃, pure Li packaged in vacuum by aluminum foil is pressed into a melt by the bell jar, and the bell jar is put out after the Li is completely melted; standing for 2min, performing secondary degassing and slag skimming, and adding a refining covering agent for the third time; standing for 5min, removing the cover layer on the surface with a ladle, and casting at 710 deg.C; the size of the finished cast ingot ranges from 100X 24mm to 300X 24mm;
b) Homogenizing annealing: homogenizing annealing the cast ingot in a vacuum atmosphere furnace, wherein the temperature error is strictly controlled to be +/-2 ℃; the application adopts a two-stage homogenizing annealing process, namely, the first stage is annealed for 8-10h at 410 ℃ and the second stage is annealed for 14-18h at 510+/-2 ℃;
c) Rolling the plate: the alloy plate is prepared by hot rolling, intermediate annealing and cold rolling;
d) Solid solution aging heat treatment: the solid solution is carried out in a salt bath furnace, and the aging treatment adopts single-stage aging and is carried out in a blast drying oven.
2. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step a, the chemical components of the experimental raw materials are pure Al 99.99 wt%, pure Mg99.99 wt%, pure Li99.9 wt%, ag99.99 wt%, and intermediate alloy Al-Cu50.0 wt%, al-Er 20.0 wt% and Al-Zr 10.0 wt%.
3. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step a, the first addition amount of the refined covering agent is 8-10g, and the second addition amount and the third addition amount are 3-4g respectively; the refining covering agent is formed by mixing LiF and LiCl in a ratio of 1:2; the addition amount of the degassing agent hexachloroethane is 6-8g each time.
4. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: and a crystallizer adopts a water-cooling copper mold during casting in the step a, and the mold is rapidly cooled by argon protection and circulating cooling water during the whole casting process.
5. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step b, the vacuum atmosphere furnace is vacuumized to 20-30Pa, and then nitrogen is introduced.
6. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step c, the homogenized alloy is subjected to head and tail cutting and surface milling treatment before rolling, the upper large surface and the lower large surface are respectively thinned by more than 1.5mm, and exposed punctiform air holes on the surfaces are cleaned by using an angle grinder.
7. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step c, before hot rolling starts, placing an ingot in an annealing furnace, preserving heat for 2-3 hours at the temperature of 450+/-10 ℃, and preheating a rolling mill roller to 120-180 ℃ by adopting a liquefied gas sprayer; in the step c, the total deformation of the hot rolling is not less than 75 percent, and the total deformation of the cold rolling is not less than 45 percent; in the step c, the sheet is subjected to intermediate annealing at 450+/-10 ℃ for about 1.5-2.5 h before cold rolling, and is cooled to room temperature along with a furnace and taken out.
8. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step d, the solid solution temperature is 520+/-1 ℃, and after the solid solution is carried out for 50-70 min, the alloy plate is immediately quenched and cooled in a water tank; the T86 sample needs to be cold-rolled and pre-deformed before aging, the deformation amount is about 6 percent, the aging is carried out at 150 ℃, and the aging time is 12 h-20 hours.
9. The corrosion-resistant high-strength and toughness Al-Li-Cu-Zr-Er alloy plate, which is characterized in that: in the step d, the water temperature of the quenching water tank is controlled to be about 25 ℃, and the quenching transfer time is less than 5s.
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| CN113215460A (en) * | 2021-04-16 | 2021-08-06 | 中南大学 | Low-density high-strength damage-resistant aluminum-lithium alloy hot rolled plate and preparation method thereof |
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| CN113215460A (en) * | 2021-04-16 | 2021-08-06 | 中南大学 | Low-density high-strength damage-resistant aluminum-lithium alloy hot rolled plate and preparation method thereof |
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