CN116287917B - Light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy and preparation method thereof - Google Patents
Light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy and preparation method thereof Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 179
- 239000000956 alloy Substances 0.000 title claims abstract description 179
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 238000001125 extrusion Methods 0.000 claims abstract description 59
- 238000003723 Smelting Methods 0.000 claims abstract description 35
- 239000012535 impurity Substances 0.000 claims abstract description 32
- 238000000137 annealing Methods 0.000 claims abstract description 27
- 238000007670 refining Methods 0.000 claims abstract description 24
- 239000006104 solid solution Substances 0.000 claims abstract description 10
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 9
- 239000000155 melt Substances 0.000 claims description 19
- 239000000243 solution Substances 0.000 claims description 18
- 238000001816 cooling Methods 0.000 claims description 16
- 239000003795 chemical substances by application Substances 0.000 claims description 14
- 238000007712 rapid solidification Methods 0.000 claims description 13
- 229910052749 magnesium Inorganic materials 0.000 claims description 12
- 238000004321 preservation Methods 0.000 claims description 12
- 239000013078 crystal Substances 0.000 claims description 11
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 10
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 10
- 239000011261 inert gas Substances 0.000 claims description 10
- AMXOYNBUYSYVKV-UHFFFAOYSA-M lithium bromide Chemical compound [Li+].[Br-] AMXOYNBUYSYVKV-UHFFFAOYSA-M 0.000 claims description 10
- KWGKDLIKAYFUFQ-UHFFFAOYSA-M lithium chloride Chemical compound [Li+].[Cl-] KWGKDLIKAYFUFQ-UHFFFAOYSA-M 0.000 claims description 10
- 239000000919 ceramic Substances 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 229910000831 Steel Inorganic materials 0.000 claims description 6
- 239000000463 material Substances 0.000 claims description 6
- 238000002156 mixing Methods 0.000 claims description 6
- 239000010959 steel Substances 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 5
- 229910018503 SF6 Inorganic materials 0.000 claims description 5
- 229910007926 ZrCl Inorganic materials 0.000 claims description 5
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 5
- 229910052786 argon Inorganic materials 0.000 claims description 5
- 238000005266 casting Methods 0.000 claims description 5
- 239000011888 foil Substances 0.000 claims description 5
- 239000007789 gas Substances 0.000 claims description 5
- 229910002804 graphite Inorganic materials 0.000 claims description 5
- 239000010439 graphite Substances 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 5
- 238000000265 homogenisation Methods 0.000 claims description 5
- HXGWMCJZLNWEBC-UHFFFAOYSA-K lithium citrate tetrahydrate Chemical compound [Li+].[Li+].[Li+].O.O.O.O.[O-]C(=O)CC(O)(CC([O-])=O)C([O-])=O HXGWMCJZLNWEBC-UHFFFAOYSA-K 0.000 claims description 5
- 229910052757 nitrogen Inorganic materials 0.000 claims description 5
- SFZCNBIFKDRMGX-UHFFFAOYSA-N sulfur hexafluoride Chemical compound FS(F)(F)(F)(F)F SFZCNBIFKDRMGX-UHFFFAOYSA-N 0.000 claims description 5
- 229960000909 sulfur hexafluoride Drugs 0.000 claims description 5
- 239000011148 porous material Substances 0.000 claims description 2
- 238000000746 purification Methods 0.000 claims 1
- 238000000034 method Methods 0.000 abstract description 12
- 238000005728 strengthening Methods 0.000 abstract description 7
- 239000006185 dispersion Substances 0.000 abstract description 6
- 239000002994 raw material Substances 0.000 abstract description 4
- 238000005204 segregation Methods 0.000 abstract description 3
- 239000011777 magnesium Substances 0.000 description 26
- 229910000861 Mg alloy Inorganic materials 0.000 description 16
- 239000011159 matrix material Substances 0.000 description 11
- 238000010586 diagram Methods 0.000 description 9
- 238000007711 solidification Methods 0.000 description 8
- 230000008023 solidification Effects 0.000 description 8
- 238000002441 X-ray diffraction Methods 0.000 description 6
- 238000001514 detection method Methods 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000001276 controlling effect Effects 0.000 description 4
- 230000010355 oscillation Effects 0.000 description 4
- 230000009286 beneficial effect Effects 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 238000005520 cutting process Methods 0.000 description 3
- 230000007547 defect Effects 0.000 description 3
- 238000005498 polishing Methods 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 150000002910 rare earth metals Chemical class 0.000 description 3
- 229910017073 AlLi Inorganic materials 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 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 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 238000013016 damping Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 238000001914 filtration Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 229910052710 silicon Inorganic materials 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 238000001179 sorption measurement Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000004781 supercooling Methods 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 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
- C22C23/00—Alloys based on magnesium
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/002—Extruding materials of special alloys so far as the composition of the alloy requires or permits special extruding methods of sequences
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D7/00—Casting ingots, e.g. from ferrous metals
- B22D7/005—Casting ingots, e.g. from ferrous metals from non-ferrous metals
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
-
- 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
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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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
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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
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C23/00—Alloys based on magnesium
- C22C23/02—Alloys based on magnesium with aluminium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/06—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of magnesium or alloys based thereon
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- Metallurgy (AREA)
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- Crystallography & Structural Chemistry (AREA)
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Abstract
The invention discloses a light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy which is prepared from the following components in percentage by mass: 5.5 to 10 percent of Li, 3.1 to 6.8 percent of Al, 0.1 to 3.7 percent of AlTiB, the ratio of Al to AlTiB is 1.8:1 to 50:1, and the balance is Mg and unavoidable impurity elements; the preparation method of the invention comprises the following steps: 1. preheating raw materials; 2. smelting; 3. refining and purifying; 4. pouring and solidifying; 5. homogenizing and annealing; 6. extruding at a low speed; 7. and (5) medium-temperature solid solution. The alloy of the invention introduces a body-centered cubic structure by controlling the addition amount of Li, combines with the addition of AlTiB to generate a dispersion strengthening phase, and obtains a light high-strength and high-toughness alloy which is suitable for bearing pressure structural members; the invention adopts constant-temperature extrusion deformation combined with medium-temperature solid solution to eliminate local component segregation, promotes coordinated deformation, improves the strength and plasticity of the alloy, and has short process flow and low cost.
Description
Technical Field
The invention belongs to the technical field of metal materials, and particularly relates to a light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy and a preparation method thereof.
Background
The magnesium alloy has the advantages of low density, high specific strength/specific rigidity and excellent damping performance and biocompatibility, so that the magnesium alloy is widely applied to the fields of aerospace, automobile industry, 3C electronics, biomedical treatment and the like as a metal structural material. Meanwhile, the magnesium alloy is of a close-packed hexagonal metal structure, and a strong basal plane texture is easy to generate in the plastic deformation process, so that the strength and the plasticity of the magnesium alloy are low, and the magnesium alloy is easy to deform and damage; the lower corrosion electrode potential and higher corrosion current density of the magnesium alloy make the corrosion resistance worse, and the magnesium alloy is easy to corrode and destroy. Therefore, many disadvantages in the performance of magnesium alloys make it difficult to realize large-scale industrial applications. Researchers in the prior art generally adopt alloying and plastic processing means, and more non-basal slip in the magnesium alloy is stimulated by regulating and controlling the texture, so that the strength and the plasticity of the magnesium alloy are synchronously improved. At present, the development hot spot of the high-performance magnesium alloy is to add Mg-Re series alloy into a magnesium matrix, but the development cost of rare earth Re is too high, the low density characteristic of the magnesium alloy cannot be ensured after the addition, and the performance of the magnesium alloy cannot be effectively improved.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides a light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy. According to the alloy, li is added and the addition amount of Li is controlled, a body-centered cubic structure is introduced into the alloy, so that the toughness of the Mg-Li-Al-TiB alloy is improved, a TiB 2 dispersion strengthening phase which belongs to the same crystal system as a Mg matrix is generated by adding AlTiB, and a good refining effect is achieved on a Mg matrix structure, so that the toughness of the Mg-Li-Al-TiB alloy is remarkably improved, the density is lower, the light weight characteristic is kept, and the problems that the strength and the plasticity of the magnesium alloy are difficult to synchronously improve and the low density characteristic cannot be guaranteed are solved.
In order to solve the technical problems, the invention adopts the following technical scheme: the light high-strength and toughness extruded Mg-Li-Al-TiB alloy is characterized by being prepared from the following components in percentage by mass: 5.5 to 10 percent of Li5.1 to 6.8 percent of Al, 0.1 to 3.7 percent of AlTiB, 1.8:1 to 50:1 percent of Al and AlTiB by mass, and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15 percent; the AlTiB consists of the following components in percentage by mass: 3.1 to 5.2 percent of Ti, 0.8 to 3.2 percent of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1 percent; the density of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 1.45g/cm 3～1.52g/cm3, the room temperature tensile strength is more than 300MPa, the room temperature yield strength is more than 250MPa, and the elongation is more than 15%.
According to the Mg-Li-Al-TiB alloy, by adding Li and strictly controlling the mass percentage of Li to be 5.5% -10%, the hcp close-packed hexagonal crystal structure (alpha matrix) part of the Mg matrix is converted into a bcc body-centered cubic structure, namely, the toughness of the Mg-Li-Al-TiB alloy is improved by introducing the body-centered cubic structure into the alloy; meanwhile, alTiB added into the Mg-Li-Al-TiB alloy is melted and then reacts in the melt to generate TiB 2 and Al 3Ti,Al3 Ti which are quickly decomposed in the melt, and a dispersion strengthening phase TiB 2 belongs to a hexagonal system and a crystal system together with an alpha matrix, so that the interface energy between the two phases is smaller, a good refining effect is achieved on the alpha matrix structure, and the solidification structure of the Mg-Li-Al-TiB alloy is obviously refined under the large-area heterogeneous nucleation effect, so that the mechanical property is obviously improved; the added Al generates second phase particles in the alloy, so that the mechanical property of the alloy is further improved; in addition, the content ratio of each element in the Mg-Li-Al-TiB alloy is controlled, so that the density of the Mg-Li-Al-TiB alloy is ensured to be lower, and the light characteristic is maintained.
The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is characterized by being prepared from the following components in percentage by mass: 6.1 to 9.8 percent of Li, 3.5 to 5.2 percent of Al, 0.1 to 1.6 percent of AlTiB and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15 percent.
The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is characterized by being prepared from the following components in percentage by mass: li 8%, al 5%, alTiB 1%, and the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B and the balance of Al and unavoidable impurity elements.
The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is characterized in that the crystal structure of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is a close-packed hexagonal structure plus a body-centered cubic structure.
In addition, the invention also provides a method for preparing the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy, which is characterized by comprising the following steps of:
step one, preheating: preheating Mg, al, alTiB intermediate alloy; the preheating temperature is 210 ℃, the preheating time is 20min, and the air cooling is carried out;
Step two, smelting: placing the pre-heated Mg, al, alTiB intermediate alloy in the step one in a No. 1 smelting furnace to be melted at 700-740 ℃ under non-vacuum conditions, placing Li in a No. 2 smelting furnace to be melted at 185-200 ℃ under non-vacuum conditions, removing scum after materials in the No. 1 smelting furnace are completely melted into a melt, inserting an ultrasonic rod, vibrating the melt by utilizing ultrasonic waves for 2min, standing for 5min, and then sending the Li liquid obtained by melting in the No. 2 smelting furnace into the No. 1 smelting furnace after ultrasonic vibration and standing under the protection of inert gas, and fully mixing with the melt to form an alloy melt;
Step three, purifying: after the temperature of the alloy melt in the second step is reduced to 690-700 ℃, adding a refining agent, then heating to 720+/-3 ℃ and preserving heat for 3-10 min for refining and purifying, removing scum, and then using ultrasonic vibration to purify the alloy melt for 2-5 min and standing for 10-16 min;
Step four, casting: pouring the alloy melt after standing in the third step into a water-cooling steel mould through a ceramic filter for rapid solidification to obtain an alloy cast ingot; the cooling rate of the rapid solidification is 150 ℃/s to 200 ℃/s;
Step five, homogenizing annealing: wrapping the alloy ingot obtained in the step four by adopting aluminum foil, and then placing the alloy ingot into an accurate numerical control muffle furnace for homogenizing annealing; the temperature of the homogenizing annealing is 300+/-2 ℃, the heat preservation time is 8-10 h, and the homogenizing annealing is cooled along with the furnace;
step six, extruding at a low speed: laying graphite paper along the inner wall of the extrusion cylinder, and then placing the alloy cast ingot subjected to the homogenization annealing in the fifth step into the extrusion cylinder for extrusion deformation to obtain an extrusion rod; the extrusion rate of the extrusion deformation is 4 mm/s-10 mm/s, the extrusion temperature is 200-300 ℃, and the extrusion ratio is 15:1;
Step seven, medium-temperature solid solution: carrying out solution treatment on the extrusion rod obtained in the step six to obtain a light high-strength and high-toughness extrusion Mg-Li-Al-TiB alloy; the temperature of the solution treatment is 250-280 ℃, the heat preservation time is 20-35 h, and the solution treatment is cooled along with the furnace.
The method comprises the steps of preheating and dewatering Mg, al, alTiB intermediate alloy with high melting point in raw materials, smelting in the same smelting furnace to obtain a melt, independently smelting Li with low melting point in the raw materials to improve the yield, mixing the Li with the melt and combining ultrasonic vibration to form uniform alloy melt, adding a high-density refining agent to refine and purify, removing impurities containing silicon, iron and nickel in the alloy melt through adsorption, filtering by a ceramic filter, removing impurities, pouring into a mold, and performing rapid solidification, and installing a water cooling device outside a steel mold to realize rapid solidification so as to enable alloy cast ingots to obtain fine grain structures; the invention continuously carries out homogenizing annealing on the alloy ingot so as to eliminate the component segregation caused by local supercooling of the alloy ingot due to rapid solidification, improve the tissue uniformity, then carries out constant-temperature extrusion deformation so as to further eliminate local defects, simultaneously promotes the sliding deformation inside the alloy ingot and the plastic strain coordination deformation among grains, brings favorable guarantee for improving the strength and the plasticity of the alloy, and further enables the dispersion strengthening phase AlLi generated in the solidification process to be fully dissolved into a matrix through medium-temperature solution treatment, so that the alloy is further strengthened after extrusion deformation, thereby obtaining the light high-strength and toughness extruded Mg-Li-Al-TiB alloy.
The method is characterized in that the inert gas in the second step is a mixed gas of argon, nitrogen and sulfur hexafluoride.
The method is characterized in that the refining agent in the third step consists of the following components in percentage by mass: 36% of LiBr, 9% of MgF, 9% of CaF, 24% of LiF, 12% of LiCl and 4% of ZrCl. The refining agent composed of the components can effectively adsorb impurities in the alloy melt, purify the alloy melt and achieve good refining effect.
The method is characterized in that the frequency of the ultrasonic vibration in the second step and the third step is 100Hz. The frequency of ultrasonic oscillation in the two-step process is controlled to refine grains, and an alloy ingot with a fine grain structure is obtained.
The method is characterized in that the internal pore diameter of the ceramic filter in the fourth step is 8-25 μm. Fine impurities and refining agents in the alloy melt are further removed by controlling the inner aperture of the ceramic filter, so that the alloy ingot is ensured to obtain a fine crystal structure.
Compared with the prior art, the invention has the following advantages:
1. according to the Mg-Li-Al-TiB alloy, the Li is added and the addition amount of the Li is controlled, so that a body-centered cubic structure is introduced into the alloy, the plasticity and toughness of the Mg-Li-Al-TiB alloy are improved, the AlTiB is added to generate a TiB 2 dispersion strengthening phase which belongs to the same crystal system as a Mg matrix, and a good refining effect is achieved on the Mg matrix structure, so that the toughness performance of the Mg-Li-Al-TiB alloy is remarkably improved, the density is lower, and the light characteristic is kept.
2. Compared with the traditional magnesium alloys such as AZ series, ZK series, rare earth series and the like, the crystal structure of the Mg-Li-Al-TiB alloy is a close-packed hexagonal structure and a body-centered cubic structure, so that the Mg-Li-Al-TiB alloy has excellent plastic property on the premise of ensuring the light weight of the Mg-Li-Al-TiB alloy, and is beneficial to subsequent plastic processing.
3. Compared with rare earth magnesium alloy, the Mg-Li-Al-TiB alloy has lower cost of raw materials of each component, reduces the development cost of the alloy and is beneficial to the application of the alloy.
4. The density of the Mg-Li-Al-TiB alloy is 1.45g/cm 3～1.52g/cm3, the room temperature tensile strength is more than 300MPa, the room temperature yield strength is more than 250MPa, the elongation is more than 15 percent, and the alloy is suitable for pressure bearing structural members on bicycles.
5. According to the preparation method disclosed by the invention, the constant-temperature extrusion deformation is combined with the medium-temperature solution treatment, so that the defect of local component segregation is effectively eliminated, the coordinate deformation of the sliding deformation inside the alloy and the plastic strain among grains is promoted, the dispersion strengthening phase AlLi is fully dissolved into a matrix to realize strengthening, and the strength and the plasticity of the Mg-Li-Al-TiB alloy are effectively improved.
6. The preparation method of the invention does not need vacuum condition, has short process flow and low cost, and is beneficial to the application and popularization of Mg-Li-Al-TiB alloy.
7. According to the invention, by controlling the composition of the refining agent in the smelting process, impurities in the alloy melt are effectively adsorbed, and the purity of the alloy melt is improved, so that a clean and impurity-free cast ingot is obtained.
The technical scheme of the invention is further described in detail through the drawings and the embodiments.
Drawings
FIG. 1 is a solidification structure diagram of an alloy ingot prepared in example 1 of the present invention.
FIG. 2 is an X-ray diffraction pattern of an alloy ingot prepared in example 1 of the present invention.
FIG. 3 is an engineering stress-engineering strain curve of a light high strength and toughness extruded Mg-Li-Al-TiB alloy prepared in example 1 of the present invention.
FIG. 4 is a solidification structure diagram of an alloy ingot prepared in example 2 of the present invention.
FIG. 5 is an X-ray diffraction pattern of an alloy ingot prepared in example 2 of the present invention.
FIG. 6 is an engineering stress-engineering strain curve of a light high strength and toughness extruded Mg-Li-Al-TiB alloy prepared in example 2 of the present invention.
FIG. 7 is a solidification structure diagram of an alloy ingot prepared in example 3 of the present invention.
FIG. 8 is an X-ray diffraction pattern of an alloy ingot prepared in example 3 of the present invention.
FIG. 9 is an engineering stress-engineering strain curve of a light high strength and toughness extruded Mg-Li-Al-TiB alloy prepared in example 3 of the present invention.
Detailed Description
Example 1
The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is prepared from the following components in percentage by mass: li 8.2%, al 4.8%, alTiB 0.1%, the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy comprises the following steps:
step one, preheating: preheating Mg, al, alTiB intermediate alloy; the preheating temperature is 210 ℃, the preheating time is 20min, and the air cooling is carried out;
Step two, smelting: placing the pre-heated Mg, al, alTiB intermediate alloy in the step one in a No. 1 smelting furnace to be melted at 740 ℃ under the non-vacuum atmosphere condition, placing Li in a No. 2 smelting furnace to be melted at 200 ℃ under the non-vacuum atmosphere condition, removing scum after materials in the No. 1 smelting furnace are completely melted into a melt, inserting an ultrasonic rod, vibrating the melt for 2min by utilizing 100Hz ultrasonic waves, standing for 5min, and then sending the Li liquid obtained by melting in the No. 2 smelting furnace into the ultrasonic vibration and standing No. 1 smelting furnace under the protection of inert gas, and fully mixing with the melt to form an alloy melt; the inert gas is mixed gas of argon, nitrogen and sulfur hexafluoride according to a volume ratio of 1:1:3;
step three, purifying: after the temperature of the alloy melt in the second step is reduced to 690-700 ℃, adding a refining agent, then heating to 720+/-3 ℃ and preserving heat for 3min for refining and purifying, removing scum, and then using 100Hz ultrasonic oscillation to purify the alloy melt for 2min and standing for 12min; the refining agent comprises the following components in percentage by mass: 36% of LiBr, 9% of MgF, 9% of CaF, 24% of LiF, 12% of LiCl and 4% of ZrCl;
step four, casting: pouring the alloy melt after standing in the third step into a water-cooling steel mould through a ceramic filter with the internal aperture of 8-25 mu m for rapid solidification to obtain an alloy cast ingot; the cooling rate of the rapid solidification is 200 ℃/s;
Step five, homogenizing annealing: wrapping the alloy ingot obtained in the step four by adopting aluminum foil, and then placing the alloy ingot into an accurate numerical control muffle furnace for homogenizing annealing; the temperature of the homogenizing annealing is 300+/-2 ℃, the heat preservation time is 10 hours, and the homogenizing annealing is cooled along with the furnace;
Step six, extruding at a low speed: paving graphite paper along the inner wall of the extrusion cylinder, cutting and polishing the alloy cast ingot subjected to the homogenization annealing in the fifth step until the surface is smooth, and then putting the alloy cast ingot into the extrusion cylinder for extrusion deformation to obtain an extrusion rod; the extrusion rate of the extrusion deformation is 6mm/s, the extrusion temperature is 300 ℃ +/-5 ℃, and the extrusion ratio is 15:1;
Step seven, medium-temperature solid solution: putting the extrusion rod obtained in the step six into a muffle furnace for solid solution treatment to obtain the light high-strength and high-toughness extrusion Mg-Li-Al-TiB alloy with the density of 1.47g/cm 3; the temperature of the solution treatment is 280 ℃, the heat preservation time is 20 hours, and the solution treatment is cooled along with a furnace.
Fig. 1 is a solidification structure diagram of an alloy ingot prepared in this example, and fig. 2 is an X-ray diffraction diagram of the alloy ingot prepared in this example, and as can be seen from fig. 1 and 2, the crystal structure of the light high strength and toughness extruded Mg-Li-Al-TiB alloy is a close-packed hexagonal structure plus a body-centered cubic structure.
Fig. 3 is an engineering stress-engineering strain curve of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy prepared in this example, and as can be seen from fig. 3, the room temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 310.8MPa, the room temperature yield strength is 264.8MPa, and the elongation is 21.5%.
Example 2
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: 7.5% of Li, 5.8% of Al, 0.5% of AlTiB, and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15%; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the high-strength and high-toughness extruded Mg-Li-Al-TiB alloy in the embodiment is different from that in the embodiment 1 in that: and step seven, the temperature of solution treatment is 265 ℃, the heat preservation time is 30 hours, and the beta-phase high-strength Mg-Li-Al-TiB alloy with the density of 1.50g/cm 3 is obtained.
Fig. 4 is a solidification structure diagram of the alloy ingot prepared in this example, and fig. 5 is an X-ray diffraction diagram of the alloy ingot prepared in this example, and as can be seen from fig. 4 and 5, the crystal structure of the light high strength and toughness extruded Mg-Li-Al-TiB alloy is a close-packed hexagonal structure plus a body-centered cubic structure.
Fig. 6 is an engineering stress-engineering strain curve of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy prepared in this example, and as can be seen from fig. 6, the room temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 311.3MPa, the room temperature yield strength is 259.8MPa, and the elongation is 17.7%.
Example 3
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: 9.3% of Li, 6.2% of Al, 1.2% of AlTiB, and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15%; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the high-strength and high-toughness extruded Mg-Li-Al-TiB alloy in the embodiment is different from that in the embodiment 1 in that: and step seven, the temperature of the solution treatment is 270 ℃, the heat preservation time is 24 hours, and the beta-phase high-strength Mg-Li-Al-TiB alloy with the density of 1.45g/cm 3 is obtained.
Fig. 7 is a solidification structure diagram of the alloy ingot prepared in this example, and fig. 8 is an X-ray diffraction diagram of the alloy ingot prepared in this example, and as can be seen from fig. 7 and 8, the crystal structure of the light high strength and toughness extruded Mg-Li-Al-TiB alloy is a close-packed hexagonal structure plus a body-centered cubic structure.
Fig. 9 is an engineering stress-engineering strain curve of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy prepared in this example, and as can be seen from fig. 9, the room temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 321.3MPa, the room temperature yield strength is 262.3MPa, and the elongation is 17.1%.
Example 4
The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is prepared from the following components in percentage by mass: li 8%, al 5%, alTiB 1%, and the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy comprises the following steps:
step one, preheating: preheating Mg, al, alTiB intermediate alloy; the preheating temperature is 210 ℃, the preheating time is 20min, and the air cooling is carried out;
Step two, smelting: placing the pre-heated Mg, al, alTiB intermediate alloy in the step one in a No. 1 smelting furnace to be melted at 720 ℃ under the non-vacuum atmosphere condition, placing Li in a No. 2 smelting furnace to be melted at 200 ℃ under the non-vacuum atmosphere condition, removing scum after materials in the No. 1 smelting furnace are completely melted into a melt, inserting an ultrasonic rod, vibrating the melt for 2min by utilizing 100Hz ultrasonic waves, standing for 5min, and then sending the Li liquid obtained by melting in the No. 2 smelting furnace into the ultrasonic vibration and standing No. 1 smelting furnace under the protection of inert gas, and fully mixing with the melt to form an alloy melt; the inert gas is mixed gas of argon, nitrogen and sulfur hexafluoride according to a volume ratio of 1:1:3;
Step three, purifying: after the temperature of the alloy melt in the second step is reduced to 690-700 ℃, adding a refining agent, then heating to 720+/-3 ℃ and preserving heat for 5min for refining and purifying, removing scum, and then using 100Hz ultrasonic oscillation to purify the alloy melt for 3min and standing for 12min; the refining agent comprises the following components in percentage by mass: 36% of LiBr, 9% of MgF, 9% of CaF, 24% of LiF, 12% of LiCl and 4% of ZrCl;
step four, casting: pouring the alloy melt after standing in the third step into a water-cooling steel mould through a ceramic filter with the internal aperture of 8-25 mu m for rapid solidification to obtain an alloy cast ingot; the cooling rate of the rapid solidification is 180 ℃/s;
step five, homogenizing annealing: wrapping the alloy ingot obtained in the step four by adopting aluminum foil, and then placing the alloy ingot into an accurate numerical control muffle furnace for homogenizing annealing; the temperature of the homogenizing annealing is 300+/-2 ℃, the heat preservation time is 9 hours, and the homogenizing annealing is cooled along with the furnace;
Step six, extruding at a low speed: paving graphite paper along the inner wall of the extrusion cylinder, cutting and polishing the alloy cast ingot subjected to the homogenization annealing in the fifth step until the surface is smooth, and then putting the alloy cast ingot into the extrusion cylinder for extrusion deformation to obtain an extrusion rod; the extrusion rate of the extrusion deformation is 8mm/s, the extrusion temperature is 280+/-5 ℃, and the extrusion ratio is 15:1;
Step seven, medium-temperature solid solution: putting the extrusion rod obtained in the step six into a muffle furnace for solid solution treatment to obtain the light high-strength and high-toughness extrusion Mg-Li-Al-TiB alloy with the density of 1.47g/cm 3; the temperature of the solution treatment is 260 ℃, the heat preservation time is 30 hours, and the solution treatment is cooled along with the furnace.
Through detection, the room-temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 329.1MPa, the room-temperature yield strength is 267.5MPa, and the elongation is 22.3%.
Example 5
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: li 10%, al 3.1%, alTiB 1%, and the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 3.1% of Ti, 0.8% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy comprises the following steps:
step one, preheating: preheating Mg, al, alTiB intermediate alloy; the preheating temperature is 210 ℃, the preheating time is 20min, and the air cooling is carried out;
Step two, smelting: placing the pre-heated Mg, al, alTiB intermediate alloy in the step one in a No. 1 smelting furnace to be melted at 700 ℃ under non-vacuum atmosphere, placing Li in a No. 2 smelting furnace to be melted at 185 ℃ under non-vacuum atmosphere, removing scum after materials in the No. 1 smelting furnace are completely melted into a melt, inserting an ultrasonic rod, vibrating the melt for 2min by utilizing 100Hz ultrasonic waves, standing for 5min, and then sending the Li liquid obtained by melting in the No. 2 smelting furnace into the No. 1 smelting furnace after ultrasonic vibration and standing under the protection of inert gas, and fully mixing with the melt to form an alloy melt; the inert gas is mixed gas of argon, nitrogen and sulfur hexafluoride according to a volume ratio of 1:1:3;
Step three, purifying: after the temperature of the alloy melt in the second step is reduced to 690-700 ℃, adding a refining agent, then heating to 720+/-3 ℃ and preserving heat for 10min for refining and purifying, removing scum, and then using 100Hz ultrasonic oscillation to purify the alloy melt for 5min and standing for 16min; the refining agent comprises the following components in percentage by mass: 36% of LiBr, 9% of MgF, 9% of CaF, 24% of LiF, 12% of LiCl and 4% of ZrCl;
Step four, casting: pouring the alloy melt after standing in the third step into a water-cooling steel mould through a ceramic filter with the internal aperture of 8-25 mu m for rapid solidification to obtain an alloy cast ingot; the cooling rate of the rapid solidification is 150 ℃/s;
Step five, homogenizing annealing: wrapping the alloy ingot obtained in the step four by adopting aluminum foil, and then placing the alloy ingot into an accurate numerical control muffle furnace for homogenizing annealing; the temperature of the homogenizing annealing is 300+/-2 ℃, the heat preservation time is 8 hours, and the homogenizing annealing is cooled along with the furnace;
step six, extruding at a low speed: paving graphite paper along the inner wall of the extrusion cylinder, cutting and polishing the alloy cast ingot subjected to the homogenization annealing in the fifth step until the surface is smooth, and then putting the alloy cast ingot into the extrusion cylinder for extrusion deformation to obtain an extrusion rod; the extrusion rate of the extrusion deformation is 4mm/s, the extrusion temperature is 250+/-5 ℃, and the extrusion ratio is 15:1;
Step seven, medium-temperature solid solution: putting the extrusion rod obtained in the step six into a muffle furnace for solid solution treatment to obtain the light high-strength and high-toughness extrusion Mg-Li-Al-TiB alloy with the density of 1.45g/cm 3; the temperature of the solution treatment is 260 ℃, the heat preservation time is 35 hours, and the solution treatment is cooled along with the furnace.
Through detection, the room-temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 305.5MPa, the room-temperature yield strength is 254.1MPa, and the elongation is 23.7%.
Example 6
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: li 5.5%, al 6.8%, alTiB 3.7%, and the balance of Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5.2% of Ti, 3.2% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the high-strength and high-toughness extruded Mg-Li-Al-TiB alloy in the embodiment is different from that in the embodiment 4 in that: the standing time in the third step is 10min; the extrusion rate of the extrusion deformation in the step six is 10mm/s; the extrusion temperature in the step six is 200+/-5 ℃; and step seven, the temperature of the solution treatment is 250 ℃, and the beta-phase high-strength Mg-Li-Al-TiB alloy with the density of 1.52g/cm 3 is obtained.
Through detection, the room-temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 331.1MPa, the room-temperature yield strength is 270.4MPa, and the elongation is 18.9%.
Example 7
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: li 6.1%, al 5.2%, alTiB 1.6%, the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the high-strength and high-toughness extruded Mg-Li-Al-TiB alloy in the embodiment is different from that in the embodiment 4 in that: the extrusion temperature in the step six is 240+/-5 ℃; and step seven, obtaining the beta-phase high-strength Mg-Li-Al-TiB alloy with the density of 1.50g/cm 3.
Through detection, the room-temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 324.5MPa, the room-temperature yield strength is 266.0MPa, and the elongation is 20.3%.
Example 8
The high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of the embodiment comprises the following components in percentage by mass: 9.8% of Li, 3.5% of Al, 0.2% of AlTiB, and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15%; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B, and the balance of Al and unavoidable impurity elements with mass percent lower than 0.1%.
The preparation method of the high-strength and high-toughness extruded Mg-Li-Al-TiB alloy in the embodiment is different from that in the embodiment 4 in that: the extrusion temperature in the step six is 250+/-5 ℃; and step seven, obtaining the beta-phase high-strength Mg-Li-Al-TiB alloy with the density of 1.46g/cm 3.
Through detection, the room-temperature tensile strength of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 306.3MPa, the room-temperature yield strength is 258.9MPa, and the elongation is 22.1%.
The above description is only of the preferred embodiments of the present invention, and is not intended to limit the present invention. Any simple modification, variation and equivalent variation of the above embodiments according to the technical substance of the invention still fall within the scope of the technical solution of the invention.
Claims (7)
1. The light high-strength and toughness extruded Mg-Li-Al-TiB alloy is characterized by being prepared from the following components in percentage by mass: 5.5-10% of Li, 3.1-6.8% of Al, 0.1-3.7% of AlTiB, 1.8:1-50:1% of Al and AlTiB by mass, and the balance of Mg and unavoidable impurity elements with mass percentage lower than 0.15%; the AlTiB consists of the following components in percentage by mass: 3.1% -5.2% of Ti, 0.8% -3.2% of B, and the balance of Al and unavoidable impurity elements with mass percentage lower than 0.1%; the density of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is 1.45g/cm 3~1.52g/cm3, the room temperature tensile strength is more than 300MPa, the room temperature yield strength is more than 250MPa, and the elongation is more than 15%; the crystal structure of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy is a close-packed hexagonal structure plus a body-centered cubic structure;
The preparation method of the light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy comprises the following steps:
step one, preheating: preheating Mg, al, alTiB intermediate alloy; the preheating temperature is 210 ℃, the preheating time is 20min, and the air cooling is carried out;
Step two, smelting: placing the pre-heated Mg, al, alTiB intermediate alloy in the step one in a No. 1 smelting furnace to be melted at 700-740 ℃ under non-vacuum conditions, placing Li in a No. 2 smelting furnace to be melted at 185-200 ℃ under non-vacuum conditions, removing scum after materials in the No. 1 smelting furnace are completely melted into a melt, inserting an ultrasonic rod, carrying out ultrasonic vibration on the melt for 2min, standing for 5min, and then sending the Li liquid obtained by melting in the No. 2 smelting furnace into the No. 1 smelting furnace after ultrasonic vibration and standing under the protection of inert gas, and fully mixing with the melt to form an alloy melt;
Step three, purifying: after the temperature of the alloy melt in the second step is reduced to 690-700 ℃, adding a refining agent, then heating to 720+/-3 ℃ and preserving heat for 3-10 min for refining purification, removing scum, and then using ultrasonic vibration to purify the alloy melt for 2-5 min and standing for 10-16 min;
step four, casting: pouring the alloy melt after standing in the third step into a water-cooling steel mould through a ceramic filter for rapid solidification to obtain an alloy cast ingot; the cooling rate of the rapid solidification is 150-200 ℃/s;
Step five, homogenizing annealing: wrapping the alloy ingot obtained in the step four by adopting aluminum foil, and then placing the alloy ingot into an accurate numerical control muffle furnace for homogenizing annealing; the temperature of the homogenizing annealing is 300+/-2 ℃, the heat preservation time is 8-10 hours, and the homogenizing annealing is cooled along with the furnace;
Step six, extruding at a low speed: laying graphite paper along the inner wall of the extrusion cylinder, and then placing the alloy cast ingot subjected to the homogenization annealing in the fifth step into the extrusion cylinder for extrusion deformation to obtain an extrusion rod; the extrusion rate of the extrusion deformation is 4-10 mm/s, the extrusion temperature is 200-300 ℃, and the extrusion ratio is 15:1;
Step seven, medium-temperature solid solution: carrying out solution treatment on the extrusion rod obtained in the step six to obtain a light high-strength and high-toughness extrusion Mg-Li-Al-TiB alloy; the temperature of the solution treatment is 250-280 ℃, the heat preservation time is 20-35 h, and the solution treatment is cooled along with the furnace.
2. The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy according to claim 1, which is characterized by comprising the following components in percentage by mass: 6.1-9.8% of Li, 3.5-5.2% of Al, 0.1-1.6% of AlTiB and the balance of Mg and unavoidable impurity elements with mass percent lower than 0.15%.
3. The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy according to claim 1, which is characterized by comprising the following components in percentage by mass: li 8%, al 5%, alTiB 1%, and the balance Mg and unavoidable impurity elements less than 0.15% by mass; the AlTiB consists of the following components in percentage by mass: 5% of Ti, 1% of B and the balance of Al and unavoidable impurity elements.
4. The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy according to claim 1, wherein the inert gas in the second step is a mixed gas of argon, nitrogen and sulfur hexafluoride.
5. The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy of claim 1, wherein in the third step, the refining agent comprises the following components in percentage by mass: 36% of LiBr, 9% of MgF, 9% of CaF, 24% of LiF, 12% of LiCl and 4% of ZrCl.
6. The light high-strength and high-toughness extruded Mg-Li-Al-TiB alloy according to claim 1, wherein the ultrasonic vibration frequencies in the second step and the third step are 100Hz.
7. The lightweight high strength and toughness extruded Mg-Li-Al-TiB alloy of claim 1, wherein the ceramic filter in step four has an internal pore size of 8 μm to 25 μm.
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