CN113249601A - Alloying method for inducing icosahedron quasicrystal phase in-situ self-generated strengthening cast aluminum-lithium alloy - Google Patents
Alloying method for inducing icosahedron quasicrystal phase in-situ self-generated strengthening cast aluminum-lithium alloy Download PDFInfo
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Abstract
An alloying method for inducing icosahedron quasicrystal phase in-situ autogenous strengthening casting of aluminum-lithium alloy relates to a method for inducing quasicrystal phase in-situ autogenous strengthening casting of aluminum-lithium alloy. The invention aims to solve the problem of delta' -Al in the existing aluminum-lithium alloy casting process3The great precipitation of Li particles will aggravate the coplanar sliding tendency, the stress concentration phenomenon at the crystal boundary is more obvious, and the obdurability of the alloy will be obviously reduced. The invention relates to an alloying method for inducing quasicrystal phase in-situ authigenic enhancement of cast aluminum-lithium alloy, which is used for strengthening Al in cast aluminum-lithium alloy by quasicrystal3While the amount of precipitated Li-strengthening particles is suppressed, the icosahedral quasicrystal phase T2‑Al6CuLi3The precipitation quantity is greatly increased, and the product of strength and elongation of the alloy is improved by more than five times.
Description
Technical Field
The invention relates to a method for casting an aluminum-lithium alloy by inducing in-situ authigenic strengthening of a quasicrystal phase.
Background
With the increasing shortage of petroleum resources and the increasing complexity of modern structural device structures, particularly in the field of high-end manufacturing of important equipment such as aerospace, military industry and the like, the development of new preparation technology and new materials is urgently needed. The aluminum-lithium alloy has the advantages of low density, high specific strength, high specific rigidity, good corrosion resistance, good fatigue resistance and the like, can reduce the weight of a component by 10 to 20 percent and improve the rigidity by 15 to 20 percent by replacing the conventional aluminum alloy, and is an ideal aerospace structural material.
Research and development of the aluminum lithium alloy is almost completely limited to the deformation aluminum lithium alloy at present. The aluminum-lithium alloy not only has excellent high specific property, but also has better casting performance, and particularly, the replication capacity of the alloy to a cavity with a fine structure is generally superior to that of a common aluminum alloy, thereby being beneficial to forming thin-walled parts for aviation; meanwhile, the allowable range of the Li content in the cast aluminum lithium alloy is wide, and the weight reduction effect of the component is more obvious. Therefore, the research on casting the aluminum lithium alloy is of great significance, the unique superiority of the casting forming technology is combined with the aluminum lithium alloy with excellent performance, and the application process of casting the aluminum lithium alloy casting in the aerospace field is expected to be accelerated. Unlike wrought alloys, cast aluminum lithium alloys cannot be pre-deformed prior to aging, and the effective precipitation strengthening phase T in the alloy1-Al2CuLi and S/S' -Al2CuMg and the like are precipitated in small quantity due to the limitation of nucleation characteristics, and the alloy basically depends on delta' -Al only3The dispersion strengthening of the Li particles limits the application range of the alloy. In addition, the biggest problem with cast aluminum-lithium alloys is their lower toughness than wrought alloys, because as the Li content of the alloy increases, δ' -Al3The great precipitation of Li particles will aggravate the coplanar sliding tendency, the stress concentration phenomenon at the grain boundary is more obvious, and the obdurability of the alloy is obviously reduced. Therefore, in order to meet the requirements of the aerospace field on light, high-strength and high-rigidity castings, the mechanical propertyThe excellent cast aluminum lithium alloy is to be researched and developed.
Disclosure of Invention
The invention provides an alloying method for inducing an icosahedron quasicrystal phase in-situ self-strengthening cast aluminum-lithium alloy, aiming at solving the technical problems that in the existing aluminum-lithium alloy casting process, a great amount of precipitation of delta' -Al3Li particles aggravates the coplanar sliding tendency, the stress concentration phenomenon at a crystal boundary is increasingly obvious, and the obdurability of the alloy is obviously reduced.
The alloying method for inducing the icosahedron quasicrystal phase in-situ autogenous strengthening cast aluminum-lithium alloy is carried out according to the following steps:
firstly, selecting pure aluminum, pure magnesium, pure lithium particles, an Al-50Cu intermediate alloy, an Al-4Zr intermediate alloy and an aluminum-based intermediate alloy containing alloying elements, and then removing surface oxide skin and a surface layer of the selected raw materials;
respectively wrapping pure magnesium and pure lithium particles by using aluminum foil;
the aluminum-based intermediate alloy containing alloying elements is Al-10Ni intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 1.8 to 3.2 percent of Li, 0.5 to 2 percent of Cu, 0.5 to 1.8 percent of Mg, 0.04 to 0.21 percent of Zr, 0.2 to 0.95 percent of Ni and the balance of Al;
the aluminum-based intermediate alloy containing the alloying elements can also be Al-4V intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 1.8 to 3.2 percent of Li, 0.5 to 2 percent of Cu, 0.5 to 1.8 percent of Mg, 0.04 to 0.21 percent of Zr, 0.2 to 0.95 percent of V, and the balance of Al;
secondly, heating the crucible to 400-420 ℃ in no-load mode, preserving heat for 2-2.5 hours, increasing the furnace temperature to 750-800 ℃, then adding the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy containing alloying elements which are weighed in the step one into the crucible, reducing the furnace temperature to 720-730 ℃ after the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy are completely melted, pressing the pure magnesium wrapped by the aluminum foil and the pure lithium particles wrapped by the aluminum foil into the melt by utilizing a graphite pressure hood, introducing protective gas, adjusting the furnace temperature to 740-750 ℃ after the alloy is completely melted, and adding C2Cl6Degassing is carried outStanding for 10-15 min, adjusting the furnace temperature to 720-725 ℃, and pouring the melt into a preheated mold to form an alloy ingot;
and thirdly, carrying out heat treatment on the alloy ingot prepared in the second step, wherein a heat treatment system is established by combining the DSC result of the ingot to obtain the aluminum-lithium alloy.
The invention provides an alloying design method for inducing quasicrystal phase in-situ autogenous enhancement of cast aluminum-lithium alloy based on an alloying induction quasicrystal phase precipitation mechanism, wherein alloying elements comprise two types: firstly, the added alloying elements can induce the icosahedron quasicrystal phase T2-Al6CuLi3Or precursor phase R-Al4.8CuLi3In-situ self-generation, reduced icosahedron quasicrystal phase T2-Al6CuLi3The external condition required for precipitation in the cast aluminum-lithium alloy can be expanded, and the range or the process condition of alloy components required for precipitation of a quasicrystal phase (or a precursor) can be expanded; secondly, the added alloying element can be doped in the icosahedron quasicrystal phase T2-Al6CuLi3In the lattice structure, the enthalpy of formation of the precipitation of the quasicrystal phase is reduced; therefore, the cast aluminum lithium alloy with enhanced in-situ self-generated quasicrystal phase is produced by using the traditional casting method, the obdurability of the cast aluminum lithium alloy can be obviously improved, and the method is suitable for preparing large-size complex-structure castings.
The icosahedron quasicrystal phase T is involved in the cast aluminum lithium alloy2-Al6CuLi3The in situ self-generated coagulation path comprises U8Type peritectic reaction:
the icosahedron quasicrystal phase T is involved in the cast aluminum lithium alloy2-Al6CuLi3The in situ self-generated coagulation path comprises U11Type peritectic reaction:
the icosahedron quasicrystal phase T is involved in the cast aluminum lithium alloy2-Al6CuLi3The in situ self-generated coagulation pathway comprises P2Type peritectic reaction:
the alloying elements can be characterized in two categories:
firstly, the intermetallic compound AlxMy (M refers to the added alloying element Ni or V) formed in the alloy after the alloying treatment has a specific lattice structure/constant, and can be used as a heterogeneous nucleation particle (similar to the adsorption effect) of a Cu/Mg-rich phase to change the alloy composition to deviate from the original solidification path, so as to induce the U8Shape, U11Type or P2Promoting the occurrence of the type solidification reaction to promote the icosahedron quasicrystal phase T2-Al6CuLi3In situ autogenesis;
secondly, the selected alloying element has the atomic radius and electronegativity similar to that of Cu, so that the alloying element is doped in the icosahedral quasicrystal phase T2-Al6CuLi3In the lattice structure, the enthalpy of formation of the precipitation of the quasicrystal phase is reduced, and the in-situ self-generation of the quasicrystal phase is promoted.
The invention relates to an alloying method for inducing quasicrystal phase in-situ authigenic enhancement of cast aluminum-lithium alloy, which is used for strengthening Al in cast aluminum-lithium alloy by quasicrystal3While the amount of precipitated Li-strengthening particles is suppressed, the icosahedral quasicrystal phase T2-Al6CuLi3The precipitation quantity is greatly increased, and the product of strength and elongation of the alloy is improved by more than five times.
The invention mainly discloses an inducible icosahedron quasicrystal phase T in aluminum lithium alloy2-Al6CuLi3The preparation of the alloy still follows the preparation process and equipment of the existing aluminum-lithium alloy by using an in-situ self-generated alloying method (including alloying element types, addition amount and the like), and the production cost of the alloy is not obviously increased.
Drawings
FIG. 1 is an Al-rich end phase diagram of an Al-Li alloy prepared in experiment I;
FIG. 2 is a TEM of the aluminum lithium alloy prepared in trial two;
FIG. 3 is a TEM of the aluminum lithium alloy prepared in run one;
FIG. 4 is a diffraction pattern of a selected area of the round bar shaped precipitated phase of FIG. 3;
FIG. 5 is a TEM atomic arrangement of the round-rod precipitated phase in FIG. 3;
FIG. 6 is a graph of engineering tensile stress-strain curves;
FIG. 7 is a comparison of the area encompassed by the alloy tensile curve.
Detailed Description
The first embodiment is as follows: the embodiment is an alloying method for inducing icosahedron quasicrystal phase in-situ spontaneous strengthening casting of aluminum-lithium alloy, which is specifically carried out according to the following steps:
firstly, selecting pure aluminum, pure magnesium, pure lithium particles, an Al-50Cu intermediate alloy, an Al-4Zr intermediate alloy and an aluminum-based intermediate alloy containing alloying elements, and then removing surface oxide skin and a surface layer of the selected raw materials;
respectively wrapping pure magnesium and pure lithium particles by using aluminum foil;
the aluminum-based intermediate alloy containing alloying elements is Al-10Ni intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 1.8 to 3.2 percent of Li, 0.5 to 2 percent of Cu, 0.5 to 1.8 percent of Mg, 0.04 to 0.21 percent of Zr, 0.2 to 0.95 percent of Ni and the balance of Al;
the aluminum-based intermediate alloy containing the alloying elements can also be Al-4V intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 1.8 to 3.2 percent of Li, 0.5 to 2 percent of Cu, 0.5 to 1.8 percent of Mg, 0.04 to 0.21 percent of Zr, 0.2 to 0.95 percent of V, and the balance of Al;
secondly, heating the crucible to 400-420 ℃ in no-load mode, preserving heat for 2-2.5 hours, raising the furnace temperature to 750-800 ℃, then adding the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy containing alloying elements which are weighed in the first step into the crucible, lowering the furnace temperature to 720 ℃ after the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy are completely meltedPressing pure magnesium wrapped by aluminum foil and pure lithium wrapped by aluminum foil into the melt by using a graphite pressing cover at the temperature of 730 ℃, introducing protective gas, adjusting the furnace temperature to 740-750 ℃ after the alloy is completely melted, and adding C2Cl6Degassing, standing for 10-15 min, adjusting the furnace temperature to 720-725 ℃, and pouring the melt into a preheated mold to form an alloy ingot;
and thirdly, carrying out heat treatment on the alloy ingot prepared in the second step to obtain the aluminum-lithium alloy.
The second embodiment is as follows: the first difference between the present embodiment and the specific embodiment is: the aluminum-based intermediate alloy containing alloying elements in the step one is Al-10Ni intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 2.51% of Li, 1.11% of Cu, 1.38% of Mg, 0.21% of Zr, 0.24% of Ni and the balance of Al. The rest is the same as the first embodiment.
The third concrete implementation mode: the present embodiment differs from the first or second embodiment in that: the aluminum-based intermediate alloy containing alloying elements in the step one is Al-10Ni intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 2.35% of Li, 0.96% of Cu, 1.22% of Mg, 0.19% of Zr, 0.44% of Ni and the balance of Al. The others are the same as in the first or second embodiment.
The fourth concrete implementation mode: the difference between this embodiment mode and one of the first to third embodiment modes is: the aluminum-based intermediate alloy containing alloying elements in the step one is Al-10Ni intermediate alloy, and the finally prepared aluminum-lithium alloy comprises the following components in percentage by mass: 2.62% of Li, 1.03% of Cu, 1.53% of Mg, 0.18% of Zr, 0.91% of Ni and the balance of Al. The rest is the same as one of the first to third embodiments.
The fifth concrete implementation mode: the fourth difference between this embodiment and the specific embodiment is that: the aluminum-based intermediate alloy containing alloying elements in the step one is Al-4V intermediate alloy, and the finally prepared aluminum-lithium alloy comprises 0.2% of V in mass fraction. The rest is the same as the fourth embodiment.
The sixth specific implementation mode: the fifth embodiment is different from the fifth embodiment in that: the method for removing the surface oxide skin and the surface layer in the first step comprises the following steps: firstly, cleaning with 0.2% NaOH aqueous solution, drying and polishing. The rest is the same as the fifth embodiment.
The seventh embodiment: the sixth embodiment is different from the sixth embodiment in that: heating the crucible to 400 ℃ in an idle load manner and preserving heat for 2 hours, increasing the furnace temperature to 750 ℃, then adding the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy containing alloying elements which are weighed in the step one into the crucible, reducing the furnace temperature to 720 ℃ after the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy are completely melted, pressing the pure magnesium wrapped by the aluminum foil and the pure lithium particles wrapped by the aluminum foil into the melt by using a graphite pressure hood, introducing protective gas, adjusting the furnace temperature to 740 ℃ after the alloy is completely melted, and adding C2Cl6Degassing, standing for 10min, adjusting the furnace temperature to 720 ℃, and pouring the melt into a preheated mold to form an alloy ingot. The rest is the same as the sixth embodiment.
The specific implementation mode is eight: the seventh embodiment is different from the seventh embodiment in that: adding C in the second step2Cl6The weight of (a) is six thousandths of the weight of the aluminum-lithium alloy. The rest is the same as the seventh embodiment.
The specific implementation method nine: the eighth embodiment is different from the eighth embodiment in that: and the protective gas in the second step is argon. The rest is the same as the embodiment eight.
The detailed implementation mode is ten: the present embodiment differs from the ninth embodiment in that: the temperature of the preheating mould in the second step is 200 ℃. The rest is the same as in the ninth embodiment.
The invention was verified with the following tests:
test one: the test is an alloying method for inducing icosahedron quasicrystal phase in-situ autogenous strengthening casting of aluminum-lithium alloy, and the test utilizes Ni alloying to induce icosahedron quasicrystal phase T2-Al6CuLi3And (3) in-situ autogenously strengthening the cast aluminum-lithium alloy, and determining the appropriate Ni alloying addition amount. The method specifically comprises the following steps:
firstly, selecting pure aluminum, pure magnesium, pure lithium particles, an Al-50Cu intermediate alloy, an Al-4Zr intermediate alloy and an aluminum-based intermediate alloy containing alloying elements, and then removing surface oxide skin and a surface layer of the selected raw materials;
respectively wrapping pure magnesium and pure lithium particles by using aluminum foil;
the aluminum-based intermediate alloy containing alloying elements is Al-10Ni intermediate alloy;
the method for removing the surface oxide skin and the surface layer in the first step comprises the following steps: firstly, cleaning the materials by using a NaOH aqueous solution with the mass concentration of 0.2%, drying the materials at 120 ℃, and polishing the materials by using No. 400 abrasive paper;
secondly, heating the crucible to 400 ℃ in an idle load manner, keeping the temperature for 2 hours, increasing the furnace temperature to 750 ℃, then adding the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy containing alloying elements which are weighed in the step one into the crucible, reducing the furnace temperature to 720 ℃ after the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy are completely melted, pressing pure magnesium wrapped by the aluminum foil and pure lithium particles wrapped by the aluminum foil into the melt by utilizing a graphite pressure hood, introducing argon, adjusting the furnace temperature to 740 ℃ after the alloy is completely melted, and adding C2Cl6Degassing, standing for 10min, adjusting the furnace temperature to 720 ℃, and pouring the melt into a preheated mold to form an alloy ingot; adding C in the second step2Cl6The weight of the aluminum-lithium alloy is six thousandth of the weight of the aluminum-lithium alloy; in the second step, the temperature of the preheated mould is 200 ℃;
and thirdly, carrying out heat treatment on the alloy ingot prepared in the second step to obtain the aluminum-lithium alloy, wherein the heat treatment process comprises solution treatment, water quenching at 25 ℃ and aging treatment, and the details are shown in Table 2.
FIG. 1 is an Al-rich end phase diagram of an Al-Li alloy prepared by experiment one (including a diagram relating to an icosahedral quasicrystal phase T)2-Al6CuLi3A self-generated coagulation path in situ).
And (2) test II: the test is a comparative test, and is different from the first test in that: in step one, no aluminum-based master alloy containing alloying elements is added, and the mass fraction of each element is different, as shown in table 1. The rest is the same as test one.
FIG. 2 is a TEM of the Al-Li alloy prepared in experiment two, and FIG. 3 is a TEM of the Al-Li alloy prepared in experiment one, from which it can be seen that experimentLarge amount of spherule delta' -Al of Al-Li alloy in test II3The Li particles (diameter about 15nm) were mostly converted into round rod-like precipitated phases (cross-sectional diameter about 35nm) in the aluminum lithium alloy in test one. FIG. 4 is a diffraction diagram of selected areas of the round rod-shaped precipitated phases in FIG. 3, and it can be seen that the diffraction spots of the round rod-shaped precipitated phases have a five-fold symmetric structure.
Using the atomic arrangement of the round-rod-shaped precipitates in the high-resolution TEM image 3, see fig. 5, the atomic structure of these precipitates was found to be a structure in which twenty atoms surround a central atom. It can be judged from FIGS. 5 and 4 that these round rod-shaped precipitated phases are icosahedral quasicrystal phases T2-Al6CuLi3. From this it was determined that Ni is an alloying element that can induce quasicrystalline phase in-situ autogenous strengthening of cast aluminum lithium alloys and that the optimum addition level should be 0.251 wt.%.
And (3) test III: the differences between this test and test one are: the mass fraction of each element in step one is different, and is shown in table 1. The rest is the same as test one.
And (4) testing: the differences between this test and test one are: the mass fraction of each element in step one is different, and is shown in table 1. The rest is the same as test one.
Fig. 6 is a graph of engineering tensile stress-strain curves, where curve 1 is the aluminum lithium alloy prepared in test two, curve 2 is the aluminum lithium alloy prepared in test one, curve 3 is the aluminum lithium alloy prepared in test three, and curve 4 is the aluminum lithium alloy prepared in test four.
Fig. 7 is a comparison graph of the area enclosed by the tensile curve of the alloy, the enclosed area is the product of strength and plasticity of the alloy, the physical meaning of the area is the comprehensive performance of the strength and plasticity of the alloy, the curve 1 is the aluminum lithium alloy prepared in the second test, and the curve 2 is the aluminum lithium alloy prepared in the first test.
TABLE 1
Note: the balance of the alloy composition is aluminum.
TABLE 2
As can be seen from Table 1, the alloying method for inducing the quasicrystal phase in-situ autogenous strengthening of the cast aluminum lithium alloy has the advantages that compared with a comparative test, the tensile strength of the quasicrystal strengthening cast aluminum lithium alloy is improved by-20 MPa, the tensile strength is improved by-50 MPa, the elongation is improved by-62.5%, and the product of strength and elongation is improved by more than five times, wherein the effect of the first test is the best.
In particular, intermetallic compound Al formed in the alloy after Ni alloying treatment3The Ni phase has an orthorhombic structure with a lattice constant of a-6.6114 nm, b-7.3662 nm, and c-4.8112 nm, and is more likely to be a Cu-rich phase (mainly Al) than an α -Al matrix (cubic structure with a lattice constant of a-b-4.0494 nm)2Heterogeneous nucleation sites (similar to the action of "adsorption" of Cu atoms in the matrix) of Cu phase, body-centered cubic structure, with lattice constants a-b-6.063 nm and c-4.872 nm, can be induced by changing the alloy composition away from the original solidification path8Promoting the occurrence of the type solidification reaction to promote the icosahedron quasicrystal phase T2-Al6CuLi3In situ self-generation.
U8Type peritectic reaction:
and (5) testing: the differences between this test and test one are: the experiment utilized V alloying to induce icosahedron quasicrystal phase T2-Al6CuLi3And (3) in-situ autogenously strengthening and casting the aluminum-lithium alloy, and determining the optimized addition amount of V alloying.
Specifically, the selected V element has an atomic radius and an electronegativity close to those of Cu as compared with an Al matrix (Cu: atomic radius 0.157nm, electronegativity 1.90; V: atomic radius 0.192nm, electronegativity 1.63; Al: atomic radius 0.182nm, electronegativity 1.61).
According to the formula of the interaction strength among elements:
in the formula, RAAnd RBAtomic radii of solute A and solvent B, NAAnd NBElectronegativity of solute A and solvent B, WA-BI.e., the strength of the interaction of element A, B, which can be used to semi-quantitatively characterize the propensity of the elements to form compounds with each other. From the above formula, WAl-V＝0.1375；WCu-V＝2.802。
It is therefore inferred that the V element is easily combined with the Cu element to form a compound, i.e., V is presumably doped in the icosahedral quasicrystal phase T2-Al6CuLi3In the lattice structure, a part of Cu atoms are replaced to occupy the central position of the lattice, the enthalpy of formation of quasi-crystalline phase precipitation is reduced, the in-situ self-generation of the quasi-crystalline phase can be promoted, and the optimal addition amount of V is 0.2 wt.%.
Claims (10)
1. An alloying method for inducing the in-situ self-generation of icosahedron quasicrystal phase to strengthen the cast Al-Li alloy features that the in-situ self-generation of icosahedron quasicrystal phase containing Li is promoted by alloying treatment to suppress delta' -Al3The large amount of Li particles are separated out, the alloy structure is more uniform, and the obdurability of the alloy can be greatly improved.
2. The alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening casting of the aluminum lithium alloy as claimed in claim 1, wherein the composition range of the aluminum lithium alloy is as follows: 1.8-3.2 wt.% Li, 0.5-2 wt.% Cu, 0.5-1.8 wt.% Mg, 0.04-0.2 wt.% Zr, and the balance alloying elements and Al.
3. The alloying method for inducing the icosahedron quasicrystal phase in-situ synthesized strengthening cast aluminum lithium alloy according to claim 1, wherein the preparation process of the alloying treatment quasicrystal phase in-situ synthesized strengthening cast aluminum lithium alloy is carried out according to the following steps:
firstly, selecting pure aluminum, pure magnesium, pure lithium particles, Al-50Cu intermediate alloy, Al-4Zr intermediate alloy and commercial aluminum-based intermediate alloy containing alloying elements, and then removing surface oxide skin and a surface layer of the selected raw materials;
respectively wrapping pure magnesium and pure lithium particles by using aluminum foil;
secondly, heating the crucible to 400-420 ℃ in no-load mode, preserving heat for 2-2.5 hours, increasing the furnace temperature to 750-800 ℃, then adding the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy containing alloying elements which are weighed in the step one into the crucible, reducing the furnace temperature to 720-730 ℃ after the pure aluminum, the Al-50Cu alloy, the Al-4Zr intermediate alloy and the aluminum-based intermediate alloy are completely melted, pressing the pure magnesium wrapped by the aluminum foil and the pure lithium particles wrapped by the aluminum foil into the melt by utilizing a graphite pressure hood, introducing protective gas, adjusting the furnace temperature to 740-750 ℃ after the alloy is completely melted, and adding C2Cl6Degassing, standing for 10-15 min, adjusting the furnace temperature to 720-725 ℃, and pouring the melt into a preheated mold to form an alloy ingot;
and thirdly, carrying out heat treatment on the alloy ingot prepared in the second step to obtain the aluminum-lithium alloy.
4. The alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening cast aluminum-lithium alloy according to claim 1, wherein the method for removing the surface scale and the surface layer in the first step is as follows: firstly, cleaning with 0.2% NaOH aqueous solution, drying and polishing;
5. the alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening cast aluminum lithium alloy as claimed in claim 1, wherein the preheating temperature of the mold in the second step is controlled at 200 ℃.
6. The alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening cast aluminum lithium alloy according to claim 1, characterized in that the heat treatment schedule in the three steps is as follows: solid solution → quenching at 25 ℃ and water quenching → aging at 175 ℃/16 h.
7. The alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening casting of aluminum lithium alloy as claimed in claim 2, wherein the aluminum lithium alloy can undergo three solidification paths, which are: (U)8Type peritectic reaction:
②U11type peritectic reaction:
③P2type peritectic reaction:
8. the alloying method for inducing the in-situ self-generation of the icosahedron quasicrystal phase to strengthen the casting of the aluminum-lithium alloy as claimed in claim 7, wherein the first type of the elements used in the alloying treatment is selected according to the random induction of the three solidification reactions to promote the in-situ self-generation of the icosahedron quasicrystal phase.
9. An alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening cast aluminum lithium alloy according to claim 1, characterized in that the standard stoichiometric ratio of the icosahedron quasicrystal phase is: al Cu Li 6:1: 3.
10. The alloying method for inducing the icosahedron quasicrystal phase in-situ spontaneous strengthening cast aluminum lithium alloy as claimed in claim 7, wherein the second type of judgment basis of the elements used in the alloying treatment is as follows: wAl-X<WCu-XWherein X represents an alloying element.
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