CN117144213A - High-comprehensive-performance aluminum lithium alloy and preparation method thereof - Google Patents
High-comprehensive-performance aluminum lithium alloy and preparation method thereof Download PDFInfo
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- 229910001148 Al-Li alloy Inorganic materials 0.000 title claims abstract description 24
- 239000001989 lithium alloy Substances 0.000 title claims abstract description 24
- JFBZPFYRPYOZCQ-UHFFFAOYSA-N [Li].[Al] Chemical compound [Li].[Al] JFBZPFYRPYOZCQ-UHFFFAOYSA-N 0.000 title claims abstract description 23
- 238000002360 preparation method Methods 0.000 title claims abstract description 10
- 239000012535 impurity Substances 0.000 claims abstract description 9
- 238000001816 cooling Methods 0.000 claims description 31
- 238000005242 forging Methods 0.000 claims description 28
- 238000005266 casting Methods 0.000 claims description 22
- 238000000034 method Methods 0.000 claims description 20
- 230000032683 aging Effects 0.000 claims description 19
- 239000000243 solution Substances 0.000 claims description 18
- 238000003825 pressing Methods 0.000 claims description 16
- 238000010791 quenching Methods 0.000 claims description 15
- 230000000171 quenching effect Effects 0.000 claims description 15
- 239000006104 solid solution Substances 0.000 claims description 13
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 12
- 229910052782 aluminium Inorganic materials 0.000 claims description 12
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 12
- 238000003723 Smelting Methods 0.000 claims description 11
- 238000007872 degassing Methods 0.000 claims description 9
- 238000001914 filtration Methods 0.000 claims description 9
- 238000000265 homogenisation Methods 0.000 claims description 9
- 229910052744 lithium Inorganic materials 0.000 claims description 8
- 229910052786 argon Inorganic materials 0.000 claims description 6
- 238000012546 transfer Methods 0.000 claims description 6
- 230000007547 defect Effects 0.000 claims description 5
- 238000007670 refining Methods 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 238000009749 continuous casting Methods 0.000 claims description 3
- 238000002844 melting Methods 0.000 claims 2
- 230000008018 melting Effects 0.000 claims 2
- 238000004519 manufacturing process Methods 0.000 claims 1
- 239000007769 metal material Substances 0.000 abstract description 2
- 239000011777 magnesium Substances 0.000 description 11
- 238000010438 heat treatment Methods 0.000 description 10
- 239000000956 alloy Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 239000000463 material Substances 0.000 description 8
- 238000004321 preservation Methods 0.000 description 8
- 229910045601 alloy Inorganic materials 0.000 description 7
- 230000005540 biological transmission Effects 0.000 description 6
- 238000001556 precipitation Methods 0.000 description 6
- 230000035882 stress Effects 0.000 description 6
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 239000002131 composite material Substances 0.000 description 4
- 238000007599 discharging Methods 0.000 description 4
- 230000001105 regulatory effect Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- WHXSMMKQMYFTQS-UHFFFAOYSA-N Lithium Chemical compound [Li] WHXSMMKQMYFTQS-UHFFFAOYSA-N 0.000 description 3
- 230000001276 controlling effect Effects 0.000 description 3
- 238000009472 formulation Methods 0.000 description 3
- 239000000203 mixture Substances 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 229910000838 Al alloy Inorganic materials 0.000 description 2
- 229910017539 Cu-Li Inorganic materials 0.000 description 2
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 238000007656 fracture toughness test Methods 0.000 description 2
- 239000007788 liquid Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 229910017073 AlLi Inorganic materials 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000002457 bidirectional effect Effects 0.000 description 1
- 238000004140 cleaning Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- OPHUWKNKFYBPDR-UHFFFAOYSA-N copper lithium Chemical compound [Li].[Cu] OPHUWKNKFYBPDR-UHFFFAOYSA-N 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000010274 multidirectional forging Methods 0.000 description 1
- AHLBNYSZXLDEJQ-FWEHEUNISA-N orlistat Chemical compound CCCCCCCCCCC[C@H](OC(=O)[C@H](CC(C)C)NC=O)C[C@@H]1OC(=O)[C@H]1CCCCCC AHLBNYSZXLDEJQ-FWEHEUNISA-N 0.000 description 1
- 239000011148 porous material Substances 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 239000002344 surface layer Substances 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Classifications
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D1/00—Treatment of fused masses in the ladle or the supply runners before casting
- B22D1/002—Treatment with gases
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
-
- 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
- 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
-
- 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
-
- 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
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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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- 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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- Crystallography & Structural Chemistry (AREA)
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Abstract
The application belongs to the technical field of nonferrous metal material preparation, and particularly relates to an aluminum-lithium alloy with high comprehensive performance and a preparation method thereof, wherein the aluminum-lithium alloy comprises the following components, by weight, 2.5-3.5% of Cu, 0.1-0.4% of Mn, 1.2-1.8% of Mg, 0.3-0.5% of Zn, less than or equal to 0.1% of Ti, 0.05-0.4% of Ag, 0.7-1.1% of Li, 0.05-0.15% of Zr, less than or equal to 0.07% of Si and less than or equal to 0.07% of Fe; the weight ratio of Cu to Mg is 1.38-2.92:1, the balance A1 and unavoidable impurities; the application effectively improves the tensile property, the fracture toughness and the anisotropy, and the comprehensive performance is obviously improved.
Description
Technical Field
The application belongs to the technical field of nonferrous metal material preparation, and particularly relates to an aluminum-lithium alloy with high comprehensive performance and a preparation method thereof.
Background
With the development of the aerospace field, the selection of suitable service materials becomes particularly important. The Al-Cu-Li alloy developed by Alcan Aerospace has excellent comprehensive performance as a third-generation Al-Li alloy, and compared with the traditional 2xxx and 7xxx aluminum alloys, the Al-Cu-Li alloy has the characteristics of low density, high rigidity, high strength and toughness matching property and the like. Every 1% of lithium is added into the alloy, the density is reduced by 3%, the elastic modulus is improved by 6%, the light high-strength cast aluminum lithium alloy is adopted to replace the conventional high-strength cast aluminum alloy, so that the structural weight is reduced by 10% -20%, the rigidity is improved by 15% -20%, the light weight of weaponry in the aviation and aerospace fields is realized, and the development requirements of high-precision, ultra-long-distance and ultra-high-speed striking are met.
For the third generation aluminum lithium alloy, the main strengthening phase is T1 (Al 2 CuLi) phase and θ' (Al 2 Cu) phase, most researchers regulate the volume fractions of T1 phase and θ' phase by controlling Cu and Li content, thereby improving the mechanical properties of the material. T1 phase nucleation energy is high, the strengthening effect is excellent, but T1 compatibility is easy to form nucleation precipitation (dislocation, grain boundary and subgrain boundary) at the defects, uneven distribution is easy to generate, meanwhile, the T1 phase belongs to an excessive second phase, so that stress plug and stress concentration can be caused, toughness, plasticity and damage resistance are not facilitated, and the bidirectional effect is realized. Therefore, in the process of pursuing precipitation strengthening, the plasticity, fracture toughness and anisotropy of the material are unstable, namely the T1 phase and the theta' phase cannot be regulated to meet the requirement of high performance. Besides the T1 phase and the theta' phase, the following precipitated phases exist in the aluminum-lithium alloy: s' (Al) 2 CuMg)、δ'（AlLi 3 ) And omega (Al) 2 A cali equilibrium state), the influence of which on the comprehensive properties of the aluminum lithium alloy is to be further studied.
Disclosure of Invention
The application aims to solve the technical problem of providing the aluminum-lithium alloy with high comprehensive performance and the preparation method thereof, which effectively improve the tensile property, the fracture toughness and the anisotropy and obviously improve the comprehensive performance.
The embodiment of the application provides an aluminum-lithium alloy with high comprehensive performance, which comprises the following components, by weight, 2.5-3.5% of Cu, 0.1-0.4% of Mn, 1.2-1.8% of Mg, 0.3-0.5% of Zn, less than or equal to 0.1% of Ti, 0.05-0.4% of Ag, 0.7-1.1% of Li, 0.05-0.15% of Zr, less than or equal to 0.07% of Si and less than or equal to 0.07% of Fe; the weight ratio of Cu to Mg is 1.38-2.92:1, the balance A1 and unavoidable impurities;
smelting and casting each component to obtain an ingot, then carrying out homogenization treatment, multidirectional upsetting, solution quenching, deep-cooling pre-pressing and aging treatment to obtain the aluminum-lithium alloy with high comprehensive performance; the deep-cooling pre-pressing method is that the forging stock after solution hardening is kept at the temperature lower than-150 ℃ for a period of time, and then three-way pre-pressing is carried out, wherein the pre-deformation degree in the three directions is 2-5%.
Preferably, the alloy comprises the following components, by weight, 2.5-3.0% of Cu, 0.1-0.3% of Mn, 1.4-1.7% of Mg, 0.3-0.5% of Zn, 0.02-0.05% of Ti, 0.05-0.3% of Ag, 0.7-1.0% of Li, 0.06-0.12% of Zr, less than or equal to 0.06% of Si and less than or equal to 0.06% of Fe; the weight ratio of Cu to Mg is 1.39-2.14:1, the balance A1 and unavoidable impurities.
The embodiment of the application provides a preparation method of an aluminum-lithium alloy with high comprehensive performance, which comprises the steps of smelting and casting each component to obtain an ingot, and then carrying out homogenization treatment, multidirectional upsetting, solution quenching, deep-cooling prepressing and aging treatment to obtain the aluminum-lithium alloy with high comprehensive performance; the deep-cooling pre-pressing method is that the forging stock after solution hardening is kept at the temperature lower than-150 ℃ for a period of time, and then three-way pre-pressing is carried out, wherein the pre-deformation degree in the three directions is 2-5%.
Preferably, the forging stock after solution hardening is kept at a temperature lower than-150 ℃ for more than 3 hours.
Preferably, the preparation method of the cast ingot comprises the steps of putting all components except Li and Ti into a smelting furnace for smelting for a period of time (2-4 h), wherein the smelting temperature is 725-745 ℃, then adding the Li and Ti components, carrying out degassing refining (the period of time is 20-30 min), deslagging, controlling the temperature of an aluminum melt to be 720-740 ℃, preferably standing for 20-40min, and then carrying out online wire feeding, degassing, filtering and casting on the aluminum melt in sequence to obtain the cast ingot.
Preferably, the online wire feeding mode adopts Al-5Ti-B for double wire feeding, and the wire feeding proportion is 2.5kg/1tAl; the degassing mode is to closely contact the aluminum melt by adopting a double rotor, and the argon flow is 7 m 3 The rotor speed is 700rpm; the filtering mode is that two-stage plate type filtering is adopted, and the pore density of a filter screen is 40-50PPi; the casting mode is to prepare a round cast ingot through a semi-continuous casting process, wherein the casting end temperature is 685-705 ℃, and the steady-state casting speed is 55-60mm/min.
Preferably, the homogenization treatment is carried out at 495-505 ℃ for 25 hours, cooling is carried out after the homogenization treatment, the cooling mode is that the temperature is 300 ℃ along with the furnace, then air cooling is carried out, and surface layer defects are removed after the temperature is cooled to below 60 ℃ (the mode is that ingot sawing and turning are carried out).
Preferably, the temperature of the multidirectional upsetting is 400-460 ℃, the deformation speed is 30-50mm/s, and the pass forging ratio is 2-5.
Preferably, the solution temperature of solution quenching is 510 ℃, the heat preservation time is 1.5h, the quenching mode is water cooling, the water temperature is 25-30 ℃, and the transfer time of solution quenching is less than 8s.
Preferably, the temperature of the aging treatment is 160-170 ℃, the temperature is kept for 10-15 hours, and then the steel is discharged from the furnace for air cooling.
The application has the beneficial effects that the second phase of the conventional aluminum-lithium alloy only regulates and controls the main strengthening phase T1 phase and the theta' phase, and the strength is increased, but the plasticity, the fracture toughness and the anisotropism of the material are not excellent due to the inversion relation, so that the defects of the prior art are overcome. The application provides a method for comprehensively improving the performance of an aluminum-lithium alloy.
The application regulates and controls the Cu/Mg proportion, ensures the precipitation of each solute atom, realizes the multi-element coexistence of a second phase, takes the T1 phase as a main part, takes the theta 'phase, the S' phase, the delta 'phase and the omega phase as reinforcements, realizes the protection against the excessive precipitation of the T1 phase and the stress concentration caused by uneven distribution (when in deformation, the T1 phase cannot be cut through from a microscopic angle and can only be bypassed), simultaneously avoids the coplanar slip caused by the excessive precipitation of the delta' phase, and the multi-element coexistence can effectively reduce the stress concentration and the coplanar slip of the alloy in the deformation process.
The heat treatment after multidirectional forging adopts a deep-cooling three-way pre-pressing mode, and is improved in the aspects of temperature field, deformation uniformity and the like compared with the traditional pre-deformation mode. Under the condition of deep cooling, the uneven deformation resistance is improved, and meanwhile, the three-dimensional compressive stress enables dislocation to be more uniform in three-dimensional space, and the two-dimensional compressive stress combined action creates conditions for uniform precipitation of multiple phases in the subsequent aging process, so that the regulated alloy has high strength, and meanwhile, the regulated alloy has good plasticity, toughness and anisotropy, and the purpose of improving comprehensive performance is achieved.
Drawings
Fig. 1 is a transmission photograph of example 1.
Fig. 2 is a transmission photograph of example 4.
Fig. 3 is a transmission photograph of comparative example 1.
Fig. 4 is a transmission photograph of comparative example 2.
Detailed Description
Example 1
The specific process flow comprises the following steps:
1) And (3) batching: the composite material consists of the following components in percentage by weight: cu:2.80%, mn:0.20%, mg:1.55%, zn:0.35%, ti:0.03%, ag:0.15%, li:0.85%, zr:0.09%, si:0.05%, fe:0.05%, wherein Cu/Mg:1.80. the balance A1 and unavoidable impurities.
2) Smelting and casting: according to the material mixing requirements, weighing aluminum ingots, magnesium ingots and other metals and heavy alloy materials with corresponding contents, putting the materials into a smelting furnace (except pure lithium ingots and aluminum-titanium intermediate alloys), vacuumizing, preheating and introducing argon into the smelting furnace before feeding, heating to 735 ℃ for smelting after feeding, obtaining a lithium-free aluminum melt after smelting for 3 hours, adjusting components in the furnace, putting the lithium ingots and the aluminum-titanium intermediate alloys into the furnace, carrying out degassing refining on the aluminum melt by adopting an inner rotor of the furnace for 20 minutes, carrying out slag skimming after finishing refining, adjusting the temperature of the aluminum melt to 730 ℃, and casting after standing for 20 minutes; before casting, cleaning the convection tank and an online system, replacing auxiliary materials, preheating, vacuumizing, introducing argon, and after casting, sequentially feeding aluminum melt on line, degassing, filtering and casting.
Feeding on line: double feeding is carried out by adopting Al-5Ti-B, and the feeding proportion is 2.5kg/1tAl;
on-line degassing: the double rotors are closely contacted with the aluminum melt, and the argon flow is 7 m 3 The rotor speed is 700rpm;
the filtering mode is as follows: adopting two-stage plate filtration, 40PPi+50PPi;
finally, the ingot is manufactured into a round ingot through a semi-continuous casting process through a casting disc. Wherein the temperature of the casting end is 690-700 ℃, and the steady casting speed is 58mm/min;
homogenizing: homogenizing heat treatment is carried out on the cast ingot, wherein the soaking furnace is a trolley type soaking furnace, argon is adopted in the furnace for atmosphere protection, the heating speed is less than 60 ℃/h, the temperature is raised to 500+/-5 ℃, the heat preservation time is 25h, the cooling mode is that the furnace door is opened to be horizontally moved out of a hearth for air cooling after the furnace is cooled to 300 ℃;
sawing and turning the sheet metal: after the soaking cast ingot is cooled to below 60 ℃, sawing and turning the cast ingot to remove surface defects;
multidirectional upsetting and pulling: heating the wagon round ingot subjected to homogenization treatment: and (5) performing multidirectional upsetting and pulling cogging treatment through a forging press. The initial forging temperature of the cast ingot is 450 ℃, the deformation speed is 40mm/s, and the pass forging ratio is 3.
Solution hardening: and (3) carrying out solid solution on the multidirectional upsetting forging stock, wherein the solid solution temperature is 510 ℃, the heat preservation time is 1.5h, the quenching mode adopts water quenching, the transfer time is less than or equal to 8 seconds, and the water temperature is 25-30 ℃.
Deep cooling and prepressing: and placing the forging stock after solid solution in a liquid nitrogen incubator at the temperature of-190 ℃ for heat preservation for 4 hours, and performing pre-three-way precompression by a forging press, wherein the pre-deformation degree in the three directions is 4%.
Aging: aging the forging stock subjected to deep-cooling pre-pressing deformation in an aging furnace, heating to 165 ℃, preserving heat for 12 hours, and then discharging and air-cooling.
Example 2
The specific process flow comprises the following steps:
1) And (3) batching: the composite material consists of the following components in percentage by weight: cu:2.60%, mn:0.20%, mg:1.65%, zn:0.35%, ti:0.03%, ag:0.15%, li:0.85%, zr:0.09%, si:0.05%, fe:0.05%, wherein Cu/Mg is 1.58. The balance A1 and unavoidable impurities.
The remaining process steps and parameters were the same as in example 1.
Example 3
1) And (3) batching: the composite material consists of the following components in percentage by weight: cu:2.95%, mn:0.20%, mg:1.45%, zn:0.35%, ti:0.03%, ag:0.15%, li:0.75%, zr:0.09%, si:0.05%, fe:0.05%, wherein Cu/Mg is 2.0. The balance A1 and unavoidable impurities.
The remaining process steps and parameters were the same as in example 1.
Example 4
The formulation and casting process were the same as in example 1.
Solution hardening: and (3) carrying out solid solution on the multidirectional upsetting forging stock, wherein the solid solution temperature is 510 ℃, the heat preservation time is 1.5h, the quenching mode adopts water quenching, the transfer time is less than or equal to 8 seconds, and the water temperature is 25-30 ℃.
Deep cooling and prepressing: and placing the forging stock after solid solution in a liquid nitrogen incubator at the temperature of-160 ℃ for heat preservation for 5 hours, and performing pre-three-way precompression by a forging press, wherein the pre-deformation degree in the three directions is 3 percent.
Aging: aging the forging stock subjected to deep-cooling pre-pressing deformation in an aging furnace, heating to 165 ℃, preserving heat for 14h, and then discharging and air-cooling.
Comparative example 1
1) And (3) batching: the composite material consists of the following components in percentage by weight: cu:4.0%, mn:0.20%, mg:0.9%, zn:0.3%, ti:0.03%, ag:0.15%, li:1.0%, zr:0.09%, si:0.05%, fe:0.05%, wherein Cu/Mg is 2.67. The balance A1 and unavoidable impurities.
The remaining process steps and parameters are nearly identical to those of example 1.
Comparative example 2
The formulation and casting process were the same as in example 1.
Solution hardening: and (3) carrying out solid solution on the multidirectional upsetting forging stock, wherein the solid solution temperature is 510 ℃, the heat preservation time is 1.5h, the quenching mode adopts water quenching, the transfer time is less than or equal to 8 seconds, and the water temperature is 25-30 ℃.
Prepressing at room temperature: the forging stock after solid solution is directly pre-compressed in three directions by a forging press, and the pre-deformation degree in the three directions is 3 percent.
Aging: aging the forging stock subjected to deep-cooling pre-pressing deformation in an aging furnace, heating to 165 ℃, preserving heat for 12 hours, and then discharging and air-cooling.
Comparative example 3
The formulation and casting process were the same as in comparative example 1.
Solution hardening: and (3) carrying out solid solution on the multidirectional upsetting forging stock, wherein the solid solution temperature is 510 ℃, the heat preservation time is 1.5h, the quenching mode adopts water quenching, the transfer time is less than or equal to 8 seconds, and the water temperature is 25-30 ℃.
Prepressing at room temperature: the forging stock after solid solution is directly pre-compressed in three directions by a forging press, and the pre-deformation degree in the three directions is 3 percent.
Aging: aging the forging stock subjected to deep-cooling pre-pressing deformation in an aging furnace, heating to 165 ℃, preserving heat for 12 hours, and then discharging and air-cooling.
The aluminum lithium forging stock prepared by the method is sampled along the X, Y, Z directions respectively, the tensile force energy test, the fracture toughness test and the transmission tissue analysis in the three directions are carried out, and finally the anisotropic data of the tensile property are counted.
The tensile properties and fracture toughness test results of each sample after processing are shown in table 1; the transmission photographs are shown in fig. 1, 2, 3 and 4, and correspond to example 1, example 4, comparative example 1 and comparative example 2, respectively.
TABLE 1
Description: anisotropy (IPA) = (2 Xmax-Xmid-Xmin)/2 xmax×100%.
As can be seen from Table 1, the aluminum-lithium alloy material provided by the application has obviously excellent tensile property, fracture toughness and anisotropy, and the comprehensive performance is obviously improved by regulating and controlling the Cu/Mg ratio and optimizing the T8 heat treatment process.
Those of ordinary skill in the art will appreciate that: the discussion of any of the embodiments above is merely exemplary and is not intended to suggest that the scope of protection of the application is limited to these examples; the technical features of the above embodiments or in the different embodiments may also be combined within the idea of the application, the steps may be implemented in any order and there are many other variations of the different aspects of one or more embodiments of the application as described above, which are not provided in detail for the sake of brevity.
One or more embodiments of the present application are intended to embrace all such alternatives, modifications and variations as fall within the broad scope of the present application. Accordingly, any omissions, modifications, equivalents, improvements and others which are within the spirit and principles of the one or more embodiments of the application are intended to be included within the scope of the application.
Claims (10)
1. The aluminum-lithium alloy with high comprehensive performance is characterized by comprising the following components, by weight, 2.5-3.5% of Cu, 0.1-0.4% of Mn, 1.2-1.8% of Mg, 0.3-0.5% of Zn, less than or equal to 0.1% of Ti, 0.05-0.4% of Ag, 0.7-1.1% of Li, 0.05-0.15% of Zr, less than or equal to 0.07% of Si and less than or equal to 0.07% of Fe; the weight ratio of Cu to Mg is 1.38-2.92:1, the balance A1 and unavoidable impurities;
smelting and casting each component to obtain an ingot, then carrying out homogenization treatment, multidirectional upsetting, solution quenching, deep-cooling pre-pressing and aging treatment to obtain the aluminum-lithium alloy with high comprehensive performance; the deep-cooling pre-pressing method is that the forging stock after solution hardening is kept at the temperature lower than-150 ℃ for a period of time, and then three-way pre-pressing is carried out, wherein the pre-deformation degree in the three directions is 2-5%.
2. The high-comprehensive-performance aluminum-lithium alloy according to claim 1, which is characterized by comprising the following components, by weight, 2.5-3.0% of Cu, 0.1-0.3% of Mn, 1.4-1.7% of Mg, 0.3-0.5% of Zn, 0.02-0.05% of Ti, 0.05-0.3% of Ag, 0.7-1.0% of Li, 0.06-0.12% of Zr, less than or equal to 0.06% of Si, and less than or equal to 0.06% of Fe; the weight ratio of Cu to Mg is 1.39-2.14:1, the balance A1 and unavoidable impurities.
3. A method for preparing the high-comprehensive-performance aluminum-lithium alloy according to claim 1 or 2, wherein each component is smelted and cast to obtain an ingot, and then the ingot is subjected to homogenization treatment, multidirectional upsetting, solution quenching, deep-cooling pre-pressing and aging treatment to obtain the high-comprehensive-performance aluminum-lithium alloy; the deep-cooling pre-pressing method is that the forging stock after solution hardening is kept at the temperature lower than-150 ℃ for a period of time, and then three-way pre-pressing is carried out, wherein the pre-deformation degree in the three directions is 2-5%.
4. The method according to claim 3, wherein the temperature of the solid solution quenched forging stock is maintained at a temperature lower than-150 ℃ for 3 hours or longer.
5. The method according to claim 3 or 4, wherein the method for producing the ingot comprises the steps of melting each component except Li and Ti in a melting furnace for a period of time at 725-745 ℃, adding the Li and Ti components, degassing and refining, skimming, controlling the temperature of the aluminum melt to 720-740 ℃, and then carrying out on-line wire feeding, degassing, filtering and casting on the aluminum melt to obtain the ingot.
6. The preparation method of claim 5, wherein the on-line wire feeding mode is double wire feeding by adopting Al-5Ti-B, and the wire feeding proportion is 2.5kg/1tAl; the degassing mode is to closely contact the aluminum melt by adopting a double rotor, and the argon flow is 7 m 3 The rotor speed is 700rpm; the filtering mode is to adopt two-stage plate type filtering; the casting mode is to prepare a round cast ingot through a semi-continuous casting process, wherein the casting end temperature is 685-705 ℃, and the steady-state casting speed is 55-60mm/min.
7. The method according to claim 3 or 4, wherein the homogenization treatment is carried out at 495-505 ℃, and the homogenization treatment is followed by cooling to 300 ℃ with the furnace, then air cooling, and removing surface defects after cooling to 60 ℃.
8. The method according to claim 3 or 4, wherein the temperature of the multidirectional upsetting is 400-460 ℃, the deformation speed is 30-50mm/s, and the pass forging ratio is 2-5.
9. The method according to claim 3 or 4, wherein the solution hardening is carried out at a solution temperature of 510 ℃ by water cooling at a water temperature of 25-30 ℃ for a transfer time of less than 8s.
10. The method according to claim 3 or 4, wherein the aging treatment is carried out at 160-170 ℃ for 10-15 hours.
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| EP0266741A1 (en) * | 1986-11-04 | 1988-05-11 | Aluminum Company Of America | Aluminium-lithium alloys and method of producing these |
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