CN114433819B - High-strength and high-toughness aluminum alloy, composite material thereof, liquid assembly preparation method and application thereof - Google Patents
High-strength and high-toughness aluminum alloy, composite material thereof, liquid assembly preparation method and application thereof Download PDFInfo
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- CN114433819B CN114433819B CN202011198232.4A CN202011198232A CN114433819B CN 114433819 B CN114433819 B CN 114433819B CN 202011198232 A CN202011198232 A CN 202011198232A CN 114433819 B CN114433819 B CN 114433819B
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D23/00—Casting processes not provided for in groups B22D1/00 - B22D21/00
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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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
- C22C49/02—Alloys containing metallic or non-metallic fibres or filaments characterised by the matrix material
- C22C49/04—Light metals
- C22C49/06—Aluminium
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Abstract
The invention discloses a high-strength and high-toughness aluminum alloy, a composite material thereof, a liquid assembly preparation method and application thereof, and relates to the technical field of metal materials. The liquid assembly preparation method comprises the following steps: impacting the high-temperature melt onto a precast block placed in a vacuum cavity under the action of pressure to obtain an aluminum alloy molten pool, and cooling and solidifying the aluminum alloy molten pool to form a semi-solid zone-melting coating; making the precast block perform three-dimensional motion, and impacting the high-temperature melt to the surface of the semisolid zone cladding layer at preset time intervals; and circularly impacting the high-strength and high-toughness aluminum alloy layer by layer and forming the composite material of the high-strength and high-toughness aluminum alloy. The method is favorable for forming a full-equiaxial fine-grained structure with uniform distribution of alloy components and uniform grain size due to small temperature gradient and high cooling speed. The method has the advantages of high preparation efficiency, low cost and obvious technical advantages. The prepared high-strength and high-toughness aluminum alloy and the composite material thereof have an ultra-fine grain structure solidification structure, and are uniform in distribution of alloy components and uniform in grain size.
Description
Technical Field
The invention relates to the technical field of metal materials, in particular to a high-toughness aluminum alloy, a composite material thereof, a liquid assembly preparation method and application thereof.
Background
The performance and the grain size of the metal material are closely related, and the grain refinement is the only technical way for simultaneously improving the strength and the plasticity of the metal material. The universal method for obtaining the nano-crystalline, the ultra-fine crystalline and the fine crystalline is to improve the strength of various metal materials in multiples, and is an important direction for the development of future metal materials. So far, the grain size of large-specification metal material products can only reach 10 microns, no method can control the grain size of large-specification metal structural materials with engineering value to be in a nanometer scale, and the performance of metal materials is far from reaching the upper limit.
Compared with the traditional coarse-grain metal material, the ultrafine-grain and nano-grain metal material has high preparation difficulty, and the grain size is difficult to be refined to below 1 mu m by common smelting casting, deformation process, conventional powder metallurgy process and the like. The current preparation methods of nano-crystal and ultra-fine crystal mainly comprise a large plastic deformation method, a powder metallurgy method, a deformation heat treatment method and the like.
The basic principle of the large plastic deformation method is that the large plastic deformation is utilized to enable crystal grains to continuously generate changes similar to recovery and recrystallization, so that the crystal grains are continuously refined, and the four processes mainly comprise equal-diameter angular extrusion, high-pressure torsion, cumulative stack rolling, multidirectional forging and the like.
The powder metallurgy method comprises the preparation and consolidation of powder, wherein the preparation of the powder mainly adopts a high-energy ball milling method. The high-energy ball milling is a process for realizing grain refinement by utilizing continuous plastic deformation of powder during ball milling, and the raw materials of the high-energy ball milling can be alloy powder or element powder, and the latter can realize mechanical alloying in the ball milling process. During high-energy ball milling, the powder is repeatedly subjected to cold welding and crushing, the deformation amount of the powder is extremely large, the dislocation density in the powder is continuously increased in the process, and when the dislocation density is increased to a certain degree, dislocation cells are gradually formed and further polygonization is carried out, so that the appearance of sub-grain boundaries or small-angle grain boundaries is caused. Finally, the deformation energy input by ball milling is converted into the interface energy of the crystal boundary, so that the refinement of the crystal grains is realized, and the effects similar to macroscopic cold deformation, recovery and recrystallization are achieved. However, since the volume fraction of the grain boundary is high, the grain tends to grow at high temperature consolidation. The traditional consolidation mode, such as free sintering, has no advantages in consolidating the powder after high-energy ball milling because the consolidation temperature is high and the consolidation time is long, which easily causes the excessive growth of crystal grains during consolidation.
The deformation heat treatment method is a process combining plastic deformation and heat treatment, and mainly utilizes recrystallization, phase change and the like of crystal grains to realize the refinement of the crystal grains, and comprises the processes of controlled cooling and controlled rolling, strain induced dynamic phase change, deformation induced phase change and the like. At present, the processes are mainly applied to the preparation of ultrafine iron and steel materials, the industrial maturity is high, part of the technologies are applied to the actual industrial production, but the materials applied by the technology are limited, and the method is not adopted for the preparation of ultrafine grained aluminum alloy.
In the additive manufacturing method represented by the laser 3D printing technology and the jet forming technology, the melting area is relatively small, so that the additive manufacturing technology can generally achieve a high cooling speed, and is favorable for forming a finer solidification structure. The technology can be used for preparing the alloy without macrosegregation, solves the problems of macrosegregation and grain form control, can also realize the direct molding of complex shapes by the laser 3D printing technology, and greatly changes the traditional forming mode of ingot casting, deformation and mechanical processing. However, the existing additive manufacturing technology for preparing nanocrystalline materials still has a technical bottleneck which is difficult to overcome from the industrial application point of view. The reason for this is that: (1) grain refinement limit: the laser 3D printing has high cooling speed, the grain size can reach 1-2 microns, but because a heat source is needed for local melting, a melting area has extremely high temperature gradient in the cooling process, so that not only a fine isometric crystal area but also a more obvious columnar crystal area exist; the temperature gradient of the spray forming technology can be well controlled, but the cooling speed is slightly lower than that of 3D printing, and the grain size can be only thinned to 10-20 microns; (2) production cost: the size of the laser 3D printed powder is tens of microns, the price is high, the product is about more than 10 times of the price of the traditional cast ingot, and meanwhile, the manufacturing cost and the maintenance cost of the laser are high; (3) ingot casting size and production efficiency: the laser 3D printing generally adopts a powder spreading and sintering method, the thickness of each layer of powder spreading is 30-50 microns, about 2 days are probably needed for printing a section of casting with the height of 200mm, and the production efficiency is unacceptable for large-scale cast ingots; (4) inherent defects of the new technology: the core of laser 3D printing and spray forming lies in the regional sintering of semi-solid materials, which easily forms a large number of loose defects in the ingot preparation process, which are unavoidable due to the technical principle defects, and which can greatly reduce the plasticity, fracture toughness and fatigue resistance of the materials.
The traditional solidification and refinement mechanism can also prepare ultra-fine grained materials, and comprises two main types of chemical methods and physical methods. Chemical methods provide a denser nucleation site primarily by the addition of grain refiners, but have limited refinement. The physical principle is that the liquid-solid interface is interfered by means of ultrasonic, electromagnetic field, mechanical stirring, etc. to change the temperature field, flow field and solute field in the liquid-solid interface or break the stably growing crystal arm to make it become new core or make the melt in the liquid-solid interface meet the growth condition of isometric crystal to promote its nucleation. However, from the practical point of view, even if the power of the external field device is large, the physical method is difficult to produce a good thinning effect because the external field effect is dispersed and cannot be concentrated at the liquid-solid interface.
In view of this, the invention is particularly proposed.
Disclosure of Invention
The invention aims to provide a liquid assembly preparation method of high-strength and high-toughness aluminum alloy and a composite material thereof, which is favorable for forming a full-equiaxial fine crystalline structure with uniform distribution of alloy components and uniform grain size due to small temperature gradient and high cooling speed. The method has the advantages of high preparation efficiency, low cost and obvious technical advantages.
The invention aims to provide a high-strength and high-toughness aluminum alloy and a composite material thereof, which have an ultra-fine grain structure solidification structure, uniform distribution of alloy components and uniform grain size.
The invention aims to provide a high-strength and high-toughness aluminum alloy and application of a composite material thereof in the field of aerospace or military industry.
The invention is realized by the following steps:
in a first aspect, the invention provides a liquid assembly preparation method of a high-strength and high-toughness aluminum alloy and a composite material thereof, which comprises the following steps:
impacting the high-temperature melt onto a precast block placed in a vacuum cavity under the action of pressure to obtain an aluminum alloy molten pool, and cooling and solidifying the aluminum alloy molten pool to form a semi-solid zone-melting coating layer;
enabling the precast block to perform three-dimensional motion, and impacting the high-temperature melt to the surface of the semi-solid zone cladding layer again at preset time intervals; and circularly impacting layer by layer to form the high-strength and high-toughness aluminum alloy and the composite material thereof.
In an alternative embodiment, the high temperature melt has a temperature of Tm + (20-30 ℃);
preferably, the temperature of the semi-solid zone-cladding layer is Tm- (100-300 ℃);
preferably, the pressure acted on the high-temperature melt is 5-20 Mpa;
preferably, the vacuum pressure in the vacuum cavity is-50 to-150 kPa.
In an alternative embodiment, the precast block has a groove structure;
preferably, the depth of the groove of the precast block is 5-10 cm;
preferably, the thickness of the precast block is 10 to 20cm.
In an alternative embodiment, preheating the precast block is further included before impacting the precast block with the high-temperature melt;
preferably, the preheating temperature of the precast block is 300-450 ℃.
In an alternative embodiment, the high-temperature melt is applied to the surface of the precast block through a nozzle to form a molten column;
preferably, the height difference between the nozzle and the precast block is 10-50 cm;
preferably, the nozzles are distributed in a plurality and array;
preferably, the number of the nozzles is 20 to 40;
preferably, the aperture of the nozzle is 0.8-2.0 mm;
preferably, the distance between any two adjacent nozzles is 5-20 mm.
In an alternative embodiment, the cooling rate of the aluminum alloy melt pool is 380 to 400 ℃/s.
In an alternative embodiment, the preset time is the interval time of high-pressure intermittent action on the high-temperature melt;
preferably, the intermittent time of the pressure acting on the high-temperature melt is adjusted according to the time required for the aluminum alloy molten pool to form a semi-solid state area after the high-temperature melt impacts on the surface of the precast block;
preferably, the track of the three-dimensional motion of the precast block is in a snake shape, and the motion speed is 100-150 mm/s.
In an alternative embodiment, the chemical composition of the high temperature melt is the same or different than the chemical composition of the precast block;
preferably, when the chemical composition of the high-temperature melt is different from that of the precast block, the chemical composition of the high-temperature melt further comprises a reinforcement;
preferably, the reinforcement comprises one or more of lithium oxide, alumina, silicon carbide, silicon nitride, boron carbide, titanium boride, aluminum borate, short fiber reinforcement;
in a second aspect, the invention provides a high-strength and high-toughness aluminum alloy and a composite material thereof, which are prepared by adopting the liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof according to any one of the foregoing embodiments;
preferably, the high-strength and high-toughness aluminum alloy and the composite material thereof are an alloy system of Al-Cu-Mg or Al-Zn-Mg-Cu.
In a third aspect, the invention provides a high-strength and high-toughness aluminum alloy and a composite material thereof, which are described in the previous embodiments, and application of the high-strength and high-toughness aluminum alloy and the composite material thereof in the aerospace or military fields.
The invention has the following beneficial effects:
the application starts from subversion of the traditional metal material ingot casting preparation method, and explores a new idea for preparing the high-strength high-toughness large-size nanocrystalline metal material based on a melt high-speed impact and rapid additive solidification method. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof utilizes the intermittent superfine high-pressure melt liquid column to strongly impact the solid phase material to enable the solid phase material to penetrate into the solid phase material to generate deep fusion with the solid phase material, greatly improves the solidification speed of the liquid metal penetrating into the solid phase material by utilizing the strong cooling effect of the original solid phase structure, and then rapidly solidifies under high supercooling degree to obtain the micron-level or even submicron-level cast grain structure. According to the liquid assembly preparation method, the high-temperature melt is impacted and acted on the surface of the precast block to form an aluminum alloy molten pool, the aluminum alloy molten pool is cooled and solidified to form a semi-solid zone-melting coating, when the molten pool is in a semi-solid zone of a primary solid phase, the high-temperature melt is utilized again to impact the precast block and the molten pool on the precast block, under the combined action of mechanical impact formed by the pressure and gravity of the high-temperature melt, thermal impact formed by the high-temperature melt and homogenization of solutes formed by stirring solid and liquid states in the motion process when the high-temperature melt acts on the precast block, the temperature field, the fluid field and the solute field at the front edge of crystal growth can be fundamentally changed, and the metal cast ingot with an ultrafine crystal structure solidification structure can be prepared by regulating and controlling the impact depth and the cooling speed. The method is favorable for forming a full-equiaxial fine-grained structure with uniform distribution of alloy components and uniform grain size due to small temperature gradient and high cooling speed. The method has the advantages of high preparation efficiency, low cost and obvious technical advantages, and the prepared high-strength and high-toughness aluminum alloy and the composite material thereof have ultra-fine grain structure solidification structures. The alloy has uniform component distribution and uniform grain size, and the microstructure comprises a nano-crystalline and ultrafine-crystalline double-scale/multi-scale, composite or gradient structure and the like. The high-strength and high-toughness aluminum alloy and the composite material thereof can be widely applied to the fields of aerospace or military industry.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
Fig. 1 is an electron microscope image of an ultrafine grained metal material prepared by a liquid assembly method according to example 1 of the present application.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. The examples, in which specific conditions are not specified, were carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are conventional products which are not indicated by manufacturers and are commercially available.
The application provides a liquid assembly preparation method of a high-strength and high-toughness aluminum alloy and a composite material thereof, which comprises the following steps:
s1, preparing high-temperature melt
According to the requirements of products, smelting the chemical components of the aluminum alloy, purifying, and then preserving the heat of the aluminum alloy melt for later use. Specifically, an induction smelting furnace can be adopted to smelt aluminum alloy, online degassing and purifying treatment is carried out, and then aluminum alloy melt is transferred into a crucible for heat preservation and standby.
For example, as a typical, non-limiting example, an Al-Cu-Mg aluminum alloy is used that has a chemical composition comprising, in mass percent: less than or equal to 0.20 percent of Si, less than or equal to 0.15 percent of Fe, 2.0 to 6.0 percent of Cu, 0.2 to 1.2 percent of Mn, 0.4 to 1.8 percent of Mg, less than or equal to 0.10 percent of Cr, 0.1 to 0.3 percent of Zn, 0.02 to 0.15 percent of Ti, less than or equal to 0.25 percent of Zr, and the balance of Al.
As a typical, non-limiting example, an Al-Zn-Mg-Cu aluminum alloy is used which has a chemical composition comprising, in mass percent: less than or equal to 0.10 percent of Si, less than or equal to 0.10 percent of Fe, 1.2 to 2.8 percent of Cu, less than or equal to 0.3 percent of Mn, 1.2 to 3.2 percent of Mg, less than or equal to 0.25 percent of Cr, 5.1 to 9.8 percent of Zn, less than or equal to 0.05 to 0.20 percent of Ti, less than or equal to 0.25 percent of Zr, and the balance of Al.
In this embodiment, the temperature of the high-temperature melt is Tm + (20-30 ℃); the temperature setting of the high-temperature melt is based on the liquid assembly process principle, the melt temperature is not too high, and the melt viscosity is reduced after the temperature of the aluminum alloy melt is far higher than the melting point, so that the aluminum alloy melt can easily flow out of a nozzle under the self-gravity. In addition, the melt with too high temperature impacts on the solid phase material, so that the splashing is serious, the high-temperature cooling is slow, and the formability of the product is poor. Therefore, the selection of 20-30 ℃ higher than the melting point (Tm) can ensure that the melt has better fluidity and uniform components, can be smoothly sprayed out under the set pressure, can form a complete molten pool in a solid phase material, and has good product formability.
S2, preheating and mounting precast block
The prefabricated block is prepared according to the chemical composition of the Al-Cu-Mg aluminum alloy or the chemical composition of the Al-Zn-Mg-Cu aluminum alloy, and then is preheated (for example, a heating furnace can be adopted to preheat the prefabricated block by a typical but non-limiting example), the preheating temperature of the prefabricated block is 300-450 ℃, and the preheated prefabricated block is transferred into a vacuum cavity.
In the embodiment of the invention, the precast block needs to be processed into a given shape in advance, a groove structure is generally adopted, which is convenient for forming a molten pool, and the solid structure at the periphery can play a role in supporting and surrounding the melt, so that the melt is prevented from splashing. The groove depth is too dark too shallow not good, and too dark post processing is troublesome, and it is big to subtract the material volume, leads to extravagant, and too shallow encloses to keep off the effect unobvious, leads to the fuse-element outflow that does not solidify, and consequently, the groove depth of prefabricated section is 5 ~ 10cm in this application and is suitable. The prefabricated block has a certain thickness, which is set according to the principle of a liquid assembly method, the intermittent superfine high-pressure melt liquid column strongly impacts the solid phase material to penetrate into the solid phase material to be deeply fused with the solid phase material, and the strong cooling effect of the original solid phase material with a certain thickness enables the liquid metal penetrating into the solid phase material to be rapidly solidified. The prefabricated section has certain thickness, and too high low not good excessively, and in this application, the thickness that preferably sets up the prefabricated section is 10 ~ 20cm, and the fuse-element can be guaranteed to best thickness and can form the molten bath of a take the altitude after interlude, plays rapid mixing's effect, and in addition, cooling effect is relevant with solid phase material thickness, and the effect that solid phase cooling and outside cooling device (water-cooling) combined together should be considered to this cooling effect.
In the embodiment of the invention, the preheating temperature of the precast block is 300-450 ℃, the preheating temperature is set according to Al-Cu-Mg series or Al-Zn-Mg-Cu series alloy, the solid phase matrix material is too hard due to too low temperature, and the high-speed melt is difficult to insert; the excessive temperature causes some phases (such as S phase and T phase) in the aluminum alloy to be dissolved or changes the appearance, structure and size of the phases, which is not beneficial to the later fusion with the solidification structure of the high-temperature melt.
S3, impacting the precast block by the high-temperature melt
Under the action of high pressure, the high-temperature melt is impacted on a precast block placed in a vacuum cavity to obtain an aluminum alloy molten pool, the aluminum alloy molten pool is cooled and solidified to form a semi-solid zone-melting coating, the cooling speed of the aluminum alloy molten pool is 380-400 ℃/s, and the temperature of the formed semi-solid zone-melting coating is Tm- (100-300 ℃).
The impact pressure acting on the high-temperature melt is 5-20 Mpa, in the embodiment of the invention, the selection of the melt impact pressure is crucial, the pressure in the upper crucible is too small to break the solid material, and the preparation of the superfine crystal material fails; the pressure is too large, the impact force is too strong, and the melt splashes and cannot be formed. The high pressure selected by the invention is 5-20 Mpa, the pressure in the range can ensure the preparation of the superfine crystal and nanocrystalline materials, and the formability of the materials can be ensured. The impact pressure of the high-temperature melt, namely the pressure generated by the high-pressure generating device, acts on the high-temperature melt through the high pressure generated by the high-pressure generating device, so that the high-temperature melt is smoothly flushed out from the nozzle.
Furthermore, the vacuum pressure in the vacuum cavity is-50 kPa to-150 kPa, and the setting of the vacuum pressure can assist the pressure at the upper part of the crucible to smoothly realize melt impact. In addition, the invention also plays a role in protecting the oxidation of a molten pool, and the superfine crystal and nano crystal materials prepared within the vacuum pressure range selected by the invention have better internal structure, lowest porosity, no oxide skin and other defects.
The high-temperature melt forms a melting column through a nozzle and acts on the surface of the precast block; the difference in height between nozzle and the prefabricated section is 10 ~ 50cm, and the size of the size direct influence impact force of this difference in height, and the difference in height is being provided with for 10 ~ 50cm in this application does benefit to and guarantees that high temperature fuse-element strikes to the prefabricated section surface smoothly and forms the molten bath, avoids the fuse-element to splash. The nozzles are distributed in an array manner; the number of nozzles, the aperture and the spacing between any two adjacent nozzles are selected as desired. The number of the nozzles is influenced by the scanning width and the size of impact stirring force in the molten pool, when the number of the nozzles is too small, the impact stirring effect in the molten pool is small, and when the number of the nozzles is too large, liquid columns formed among the nozzles can interfere with each other to reduce the impact force. The size of the nozzle directly determines the impact force, so that the formation of ultrafine grains is influenced, and under a certain pressure, the nozzle is too large, the generated impact force is small, and on the contrary, the impact force is large. In addition, the nozzle is too small, so that impurities in the melt block the nozzle, and the high-temperature melt is easy to overflow under the action of the dead weight because the nozzle is too large. The distance between any two adjacent nozzles is beneficial to enabling a molten pool formed after the high-temperature melt impacts the precast block to form a whole, a plurality of mutually independent molten pools cannot appear, and a molten channel cannot be formed.
Preferably, the number of the nozzles in the present application is 20 to 40; the aperture of the nozzle is 0.8-2.0 mm; the distance between any two adjacent nozzles is 5-20 mm.
Because the temperature of high temperature fuse-element is higher than the temperature of prefabricated section, the high temperature fuse-element is when assaulting the prefabricated section, the aluminum alloy molten bath can realize solidifying under the strong cooling effect that receives the solid phase tissue of prefabricated section, in order to accelerate the solidification rate of aluminum alloy molten bath, set up cooling device in the vacuum cavity in this application, and place the prefabricated section on cooling device's surface, operate like this, can realize making the aluminum alloy molten bath receive the combined action of the strong cooling of prefabricated section solid phase tissue and cooling device simultaneously, solidify fast, refrigerated speed can reach 380 ~ 400 ℃/s.
Particularly, cooling device in this application mainly used cools off the prefabricated section of placing in its surface, and cooling device also is groove structure, can realize better holding the prefabricated section. This cooling device adopts water-cooled form to cool off the prefabricated section, can be so that after the high temperature fuse-element impacted the prefabricated section, the temperature of prefabricated section reduced fast, more was favorable to making the liquid metal rapid solidification vibration material disk.
S4, circulating layer-by-layer impact
Making the precast block perform three-dimensional motion, and impacting the high-temperature melt to the surface of the semisolid zone cladding layer at preset time intervals; and circularly impacting layer by layer to form the high-strength and high-toughness aluminum alloy and the composite material thereof.
Utilize three-dimensional telecontrol equipment to drive the prefabricated section and carry out three-dimensional motion in this application, particularly, in this application, three-dimensional telecontrol equipment sets up in the vacuum cavity, three-dimensional telecontrol equipment is the platform form in this application, cooling device installs in three-dimensional telecontrol equipment's surface, the prefabricated section is placed in cooling device's surface, three-dimensional telecontrol equipment can drive cooling device and prefabricated section simultaneously and carry out three-dimensional motion, make the high temperature fuse-element can realize strikeing the different positions of prefabricated section, so that the molten bath that forms presents a whole, the condition of gully can not appear.
Specifically, in the present application, the motion trajectory of the three-dimensional motion device is a snake shape, and the motion speed is 100 to 150mm/s. When the semi-solid zone-melting coating layer on the precast block accumulates a certain thickness, the precast block can be driven to move downwards by the three-dimensional movement device so as to adjust the spacing distance between the nozzle and the precast block, thereby ensuring the optimal impact effect.
The structure of the three-dimensional motion device in the present application is not specifically described in the present application, and the structure thereof can refer to the prior art as long as the prefabricated section can be driven to perform three-dimensional motion.
The preset time in the application is the interval time of high-pressure intermittent action on the high-temperature melt; preferably, the intermittent time of the pressure applied to the high-temperature melt is adjusted by the time required for the molten pool of the aluminum alloy to form a semi-solid state region after the high-temperature melt impacts the surface of the preform. More specifically, when the temperature of the aluminum alloy molten pool is reduced to the temperature of a semi-solid region formed by a primary solid phase, the second-pass high-pressure melt just scans the surface of a cladding layer in the semi-solid region to perform mechanical interference on the semi-solid region.
Further, the chemical composition of the high-temperature melt is the same as or different from that of the precast block.
When the chemical composition of the high-temperature melt is the same as that of the prefabricated block, the finally formed product is an aluminum alloy material, and when the chemical composition of the high-temperature melt is different from that of the prefabricated block, the finally formed product is an aluminum-based composite material.
Specifically, when the chemical composition of the high-temperature melt is different from that of the precast block, the chemical composition of the high-temperature melt also comprises a reinforcement; the arrangement of the reinforcement body can enhance the impact effect of the high-temperature melt on the precast block and can selectively change the performance of the final product. Preferably, the reinforcement comprises one or more of lithium oxide, alumina, silicon carbide, silicon nitride, boron carbide, titanium boride, aluminium borate, short fibre reinforcement.
It should be noted that the technical term "liquid assembly" in the present application means that a liquid state of a high-temperature melt is impacted onto the surface of a solid precast block, so that a liquid column is strongly impacted into the precast block to be deeply fused with the precast block, and the solidification speed of the liquid metal penetrating through the precast block is greatly increased by using the strong cooling effect of the original solid phase structure, and then the liquid metal is rapidly solidified at a high supercooling degree to obtain a micron-level or even submicron-level cast grain structure, so as to prepare the high-strength and high-toughness aluminum alloy and the composite material thereof.
The high-strength and high-toughness aluminum alloy and the composite material thereof prepared by the liquid assembly preparation method have the advantages that the alloy components are uniformly distributed, the grain size is uniform, and the microstructure comprises a nanocrystalline and ultrafine-grained dual-scale/multi-scale, composite or gradient structure and the like. Preferably, the high-strength and high-toughness aluminum alloy and the composite material thereof are an alloy system of Al-Cu-Mg or Al-Zn-Mg-Cu. The high-strength and high-toughness aluminum alloy and the composite material thereof can be widely applied to the fields of aerospace or military industry.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
Base material: an induction smelting furnace is adopted to smelt Al-Cu-Mg series aluminum alloy, the temperature of the high-temperature melt is Tm +20 ℃, and a uniform and pure high-temperature aluminum alloy melt is obtained.
An Al-Cu-Mg series aluminum alloy precast block is adopted, the thickness of the precast block is 10cm, the precast block is in a groove structure, and the depth of the groove is 5cm; preheating an aluminum alloy precast block by using a heating furnace at the preheating temperature of 300 ℃, and mounting the precast block on a condenser on a three-dimensional motion platform after preheating; 20 nozzles which are arranged in an array and have the aperture of 0.8mm are adopted, and the distance between any two adjacent nozzles is 10mm.
The liquid assembly process comprises the following steps: under the conditions that the impact pressure of a melt is 5Mpa and the vacuum pressure in a vacuum cavity is-50 kPa, a high-temperature melt is sprayed out from a crucible through a plurality of nozzles and impacts a precast block which is doing three-dimensional motion to obtain an aluminum alloy molten pool, wherein the three-dimensional motion track is in a snake shape, the motion speed is 100mm/s, the aluminum alloy molten pool is rapidly solidified under the combined action of forced cooling of a solid phase structure of the precast block and a cooling device, the cooling speed is 380 ℃/s, the temperature of a formed semisolid zone-melting coating layer is Tm-100 ℃, when the temperature of the aluminum alloy molten pool is reduced to a semisolid zone formed by a primary solid phase, a second-pass high-pressure melt just sweeps the surface of the semisolid zone-melting coating layer to perform mechanical interference on the semisolid zone-melting coating layer, and then is cooled until a double-scale/multi-scale nanocrystalline, ultrafine crystal and fine crystal aluminum alloy part is formed after the semisolid zone-melting coating layer is acted in a circulating layer-by layer manner.
Taking out and cutting a sample: and taking the prepared aluminum alloy piece out of the platform, removing the edges of the surrounding precast blocks, cutting the aluminum alloy piece into a set shape according to the requirement, and carrying out later rolling deformation treatment to obtain the T3-state Al-Cu-Mg series aluminum alloy material.
Example 2:
base material: an induction smelting furnace is adopted to smelt Al-Cu-Mg series aluminum alloy, the temperature of the high-temperature melt is Tm +30 ℃, and a uniform and pure high-temperature aluminum alloy melt is obtained.
An Al-Cu-Mg series aluminum alloy precast block is adopted, the thickness of the precast block is 20cm, the precast block is in a groove structure, and the depth of the groove is 10cm; preheating the aluminum alloy precast block by a heating furnace at the preheating temperature of 450 ℃, and mounting the precast block on a condenser on a three-dimensional motion platform after preheating; 40 nozzles which are arranged in an array and have the aperture of 1.2mm are adopted, and the distance between any two adjacent nozzles is 10mm.
The liquid assembly process comprises the following steps: under the conditions that the impact pressure of the melt is 20Mpa and the vacuum pressure in a vacuum cavity is-150 kPa, high-temperature melt is sprayed out of the crucible through a plurality of nozzles and impacts on a precast block which is doing three-dimensional motion to obtain an aluminum alloy molten pool, wherein the three-dimensional motion track is in a snake shape, the motion speed is 150mm/s, the aluminum alloy molten pool is rapidly solidified under the combined action of forced cooling of a solid phase structure of the precast block and a cooling device, the cooling speed is 400 ℃/s, the temperature of a formed semisolid zone-melting coating layer is Tm-300 ℃, when the temperature of the aluminum alloy molten pool is reduced to a semisolid zone formed by a primary solid phase, the second-pass high-pressure melt just sweeps the surface of the semisolid zone-melting coating layer to perform mechanical interference on the semisolid zone-melting coating layer, and then the semisolid zone-melting coating layer is cyclically acted layer by layer, and then is cooled until double-scale/multi-scale nano-crystal, ultra-fine crystal and fine crystal aluminum alloy pieces are formed.
Taking out and cutting a sample: and taking the prepared aluminum alloy piece out of the platform, removing the edges of the surrounding precast blocks, cutting the aluminum alloy piece into a set shape according to the requirement, and carrying out later rolling deformation treatment to obtain the T3-state Al-Cu-Mg series aluminum alloy material.
Example 3:
base material: an induction smelting furnace is adopted to smelt Al-Zn-Mg-Cu aluminum alloy, the temperature of the high-temperature melt is Tm +20 ℃, and a uniform and purified high-temperature aluminum alloy melt is obtained.
Adopting an Al-Zn-Mg-Cu series aluminum alloy precast block, wherein the thickness of the precast block is 10cm, the precast block is in a groove structure, and the depth of the groove is 5cm; preheating an aluminum alloy precast block by using a heating furnace at the preheating temperature of 300 ℃, and mounting the precast block on a condenser on a three-dimensional motion platform after preheating; 20 nozzles which are arranged in an array and have the aperture of 0.8mm are adopted, and the distance between any two adjacent nozzles is 5mm.
The liquid assembly process comprises the following steps: under the conditions that the impact pressure of a melt is 5Mpa and the vacuum pressure in a vacuum cavity is-50 kPa, a high-temperature melt is sprayed out from a crucible through a plurality of nozzles and impacts a precast block which is doing three-dimensional motion to obtain an aluminum alloy molten pool, wherein the three-dimensional motion track is in a snake shape, the motion speed is 100mm/s, the aluminum alloy molten pool is rapidly solidified under the combined action of forced cooling of a solid phase structure of the precast block and a cooling device, the cooling speed is 380 ℃/s, the temperature of a formed semisolid zone-melting coating layer is Tm-100 ℃, when the temperature of the aluminum alloy molten pool is reduced to a semisolid zone formed by a primary solid phase, a second-pass high-pressure melt just sweeps the surface of the semisolid zone-melting coating layer to perform mechanical interference on the semisolid zone-melting coating layer, and then is cooled until a double-scale/multi-scale nanocrystalline, ultrafine crystal and fine crystal aluminum alloy part is formed after the semisolid zone-melting coating layer is acted in a circulating layer-by layer manner.
Taking out and cutting a sample: and taking the prepared aluminum alloy piece out of the platform, removing the edges of the surrounding precast blocks, cutting the aluminum alloy piece into a set shape according to the requirement, and performing later rolling deformation processing to obtain the T6-state Al-Zn-Mg-Cu aluminum alloy.
Example 4:
base material: an induction smelting furnace is adopted to smelt Al-Zn-Mg-Cu aluminum alloy, the temperature of the high-temperature melt is Tm +30 ℃, and a uniform and pure high-temperature aluminum alloy melt is obtained.
Adopting an Al-Zn-Mg-Cu series aluminum alloy precast block, wherein the thickness of the precast block is 20cm, the precast block is in a groove structure, and the depth of the groove is 10cm; preheating the aluminum alloy precast block by a heating furnace at the preheating temperature of 450 ℃, and mounting the precast block on a condenser on a three-dimensional motion platform after preheating; 40 nozzles which are arranged in an array and have the aperture of 1.2mm are adopted, and the distance between any two adjacent nozzles is 5mm.
The liquid assembly process comprises the following steps: under the conditions that the impact pressure of the melt is 20Mpa and the vacuum pressure in a vacuum cavity is-150 kPa, the high-temperature melt is sprayed out from the crucible through a plurality of nozzles and impacted on a precast block which is doing three-dimensional motion to obtain an aluminum alloy molten pool, wherein the three-dimensional motion track is in a snake shape, the motion speed is 150mm/s, the aluminum alloy molten pool is rapidly solidified under the combined action of forced cooling of a solid phase structure of the precast block and a cooling device, the cooling speed is 400 ℃/s, the temperature of a formed semi-solid zone-melting coating layer is Tm-300 ℃, when the temperature of the aluminum alloy molten pool is reduced to a semi-solid zone formed by a primary solid phase, the high-pressure melt of a second pass just sweeps across the surface of the semi-solid zone-melting coating layer to perform mechanical interference on the semi-solid zone melting coating layer, and then is cooled until double-scale/multi-scale nanocrystalline, ultrafine crystal and fine crystal aluminum alloy parts are formed after the semi-solid zone melting coating layer is acted layer by layer circularly.
Taking out and cutting a sample: and taking the prepared aluminum alloy piece out of the platform, removing the edges of the surrounding precast blocks, cutting the aluminum alloy piece into a set shape according to the requirement, and performing later rolling deformation processing to obtain the T6-state Al-Zn-Mg-Cu aluminum alloy.
Example 5
Base material: melting Al-Zn-Mg-Cu-10% SiC-granule reinforced aluminum alloy by using an induction melting furnace, wherein the temperature of the high-temperature melt is Tm +100 ℃, and obtaining a uniform and purified high-temperature aluminum alloy melt.
Adopting an Al-Zn-Mg-Cu series aluminum alloy precast block, wherein the thickness of the precast block is 20cm, the precast block is in a groove structure, and the depth of the groove is 10cm; preheating the aluminum alloy precast block by a heating furnace at the preheating temperature of 450 ℃, and mounting the precast block on a condenser on a three-dimensional motion platform after preheating; 40 nozzles which are arranged in an array and have the aperture of 2.0mm are adopted, and the distance between any two adjacent nozzles is 10mm.
The liquid assembly process comprises the following steps: under the conditions that the impact pressure of the melt is 20Mpa and the vacuum pressure in a vacuum cavity is-150 kPa, high-temperature melt is sprayed out of the crucible through a plurality of nozzles and impacts on a precast block which is doing three-dimensional motion to obtain an aluminum alloy molten pool, wherein the three-dimensional motion track is in a snake shape, the motion speed is 150mm/s, the aluminum alloy molten pool is rapidly solidified under the combined action of forced cooling of a solid phase structure of the precast block and a cooling device, the cooling speed is 400 ℃/s, the temperature of a formed semisolid zone-melting coating layer is Tm-300 ℃, when the temperature of the aluminum alloy molten pool is reduced to a semisolid zone formed by a primary solid phase, the second-pass high-pressure melt just sweeps the surface of the semisolid zone-melting coating layer to perform mechanical interference on the semisolid zone-melting coating layer, and then the semisolid zone-melting coating layer is cyclically acted layer by layer, and then is cooled until double-scale/multi-scale nano-crystal, ultra-fine crystal and fine crystal aluminum alloy pieces are formed.
Taking out and cutting a sample: and taking the prepared aluminum alloy piece out of the platform, removing the edges of the surrounding prefabricated blocks, cutting the aluminum alloy piece into a set shape according to the requirement, and performing later rolling deformation processing to obtain the T6-state Al-Zn-Mg-Cu aluminum alloy.
Comparative example 1: and performing later rolling deformation treatment on the Al-Cu-Mg series aluminum alloy cast ingot prepared by adopting a conventional DC casting method to obtain the T3-state Al-Cu-Mg series aluminum alloy.
Comparative example 2: and carrying out later rolling deformation treatment on the Al-Zn-Mg-Cu aluminum alloy cast ingot prepared by adopting a conventional DC casting method to obtain the T6-state Al-Zn-Mg-Cu aluminum alloy material.
Comparative example 3: this comparative example is substantially the same as example 1 except that in this comparative example, the cooling apparatus of example 1 is omitted, and the cooling rate of the molten pool of aluminum alloy is 5 ℃/s.
Comparative example 4: the comparative example is basically the same as example 1 except that the impact pressure in the crucible where the high-temperature melt is located in the comparative example is 0MPa, and the melt flows onto the precast block by the self-weight and the negative pressure in the vacuum chamber.
Mechanical property tests were performed on the examples and comparative examples, and the test results are shown in the following table:
an electron microscope image of the high-strength and high-toughness aluminum alloy material prepared in the embodiment 1 can refer to fig. 1, and the fig. 1 shows that the grain size of the high-strength and high-toughness aluminum alloy material is distributed from hundreds of nanometers to several micrometers, so that the high-strength and high-toughness aluminum alloy material prepared by the liquid assembly preparation method provided by the application is fully proved to be a double-scale/multi-scale nanocrystalline, ultrafine-crystal and fine-crystal aluminum alloy part and to have a micron-scale or even submicron-scale cast grain structure. However, the size of the grain structure directly affects the strength and plasticity of the aluminum alloy material.
As can be seen from the above table, the greater the melt impact pressure and the greater the vacuum degree in the vacuum chamber, the higher the tensile strength, yield strength and elongation of the aluminum alloy material formed by impact. Comparing examples 1-2 with comparative example 1, and comparing examples 3-4 with comparative example 2, it can be seen that the mechanical properties of the ultra-fine grain and nano-grain aluminum alloy material prepared by the invention are improved by 50% and the elongation is improved by 60% compared with the conventional method. In the comparative example 3, the cooling device in the example 1 is omitted, so that a molten pool formed by impacting the precast block by the high-temperature melt is solidified only by the cooling effect of a solid phase structure, the cooling speed is high at first, along with the gradual material increase from layer to layer, the cooling speed of the molten pool is slow, crystal grains grow into a dendritic shape gradually, the size of the crystal grains in the final material is large, the subsequent deformation and the genetic coarse-grained characteristic in the heat treatment process are caused, and the tensile strength and the yield strength of the material are far lower than those of the molten pool in the example 1. It can be seen from comparative example 4 that when the high-temperature melt flows onto the precast block through the dead weight and the negative pressure in the vacuum chamber, the high-temperature melt cannot strongly impact the precast block, and further, the high-temperature melt is difficult to penetrate into the solid phase material of the precast block, strong stirring and deep fusion of the melt cannot occur, the high-temperature melt is only stacked on the surface of the precast block layer by layer, and the tensile strength, the yield strength and the elongation are all obviously less than those of example 1.
In addition, the SiC particle reinforced aluminum alloy is adopted as the high-temperature melt in the example 5 provided by the application, and the finally formed material is the aluminum alloy composite material, and the research of the inventor finds that the composite material has higher service temperature, modulus and strength, increased thermal stability and better abrasion resistance compared with the unreinforced alloy.
In conclusion, the method starts from subverting the traditional metal material ingot casting preparation method, and explores a new idea for preparing the high-strength high-toughness large-size nanocrystalline metal material based on a melt high-speed impact and rapid additive solidification method. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof utilizes the intermittent superfine high-pressure melt liquid column to strongly impact the solid phase material to enable the solid phase material to penetrate into the solid phase material to generate deep fusion with the solid phase material, greatly improves the solidification speed of the liquid metal penetrating into the solid phase material by utilizing the strong cooling effect of the original solid phase structure, and then rapidly solidifies under high supercooling degree to obtain the micron-level or even submicron-level cast grain structure. According to the liquid assembly preparation method, the high-temperature melt is impacted and acted on the surface of the precast block to form an aluminum alloy molten pool, the aluminum alloy molten pool is cooled and solidified to form a semi-solid zone-melting coating, when the molten pool is in a semi-solid zone of a primary solid phase, the high-temperature melt is utilized again to impact the precast block and the molten pool on the precast block, under the combined action of mechanical impact formed by the pressure and gravity of the high-temperature melt, thermal impact formed by the high-temperature melt and homogenization of solutes formed by stirring solid and liquid states in the motion process when the high-temperature melt acts on the precast block, the temperature field, the fluid field and the solute field at the front edge of crystal growth can be fundamentally changed, and the metal cast ingot with an ultrafine crystal structure solidification structure can be prepared by regulating and controlling the impact depth and the cooling speed. The method is favorable for forming a full-equiaxial fine-grained structure with uniform distribution of alloy components and uniform grain size due to small temperature gradient and high cooling speed. The method has the advantages of high preparation efficiency, low cost and obvious technical advantages, and the prepared high-strength and high-toughness aluminum alloy and the composite material thereof have an ultrafine-grained structure solidification structure. The alloy has uniform component distribution and uniform grain size, and the microstructure comprises a nano-crystalline and ultrafine-crystalline double-scale/multi-scale, composite or gradient structure and the like. The high-strength and high-toughness aluminum alloy and the composite material thereof can be widely applied to the fields of aerospace or military industry.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (22)
1. A liquid assembly preparation method of high-strength and high-toughness aluminum alloy and composite material thereof is characterized by comprising the following steps:
impacting the high-temperature melt onto a precast block placed in a vacuum cavity under the action of pressure to obtain an aluminum alloy molten pool, and cooling and solidifying the aluminum alloy molten pool to form a semi-solid zone-melting coating layer;
enabling the precast block to perform three-dimensional motion, and impacting the high-temperature melt to the surface of the semi-solid zone cladding layer again at preset time intervals; circularly impacting layer by layer to form the high-strength and high-toughness aluminum alloy and the composite material thereof;
the temperature of the high-temperature melt is Tm + (20-30 ℃); the temperature of the semi-solid zone melting coating is Tm- (100-300 ℃); the pressure acted on the high-temperature melt is 5-20 Mpa; the vacuum pressure in the vacuum cavity is-50 to-150 kPa.
2. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 1, wherein the precast block is of a groove structure.
3. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 2, wherein the groove depth of the precast block is 5-10 cm.
4. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 2, wherein the thickness of the precast block is 10-20 cm.
5. The method for liquid assembly preparation of high-strength and high-toughness aluminum alloy and composite material thereof according to claim 1, further comprising preheating the precast block before impacting the precast block with the high-temperature melt.
6. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 5, wherein the preheating temperature of the precast block is 300-450 ℃.
7. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 1, wherein the high-temperature melt is formed into a molten column through a nozzle and acts on the surface of the precast block.
8. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 7, wherein the height difference between the nozzle and the precast block is 10-50 cm.
9. The liquid assembly preparation method of high strength and toughness aluminum alloy and composite material thereof according to claim 7, wherein the nozzles are distributed in a plurality of arrays.
10. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 9, wherein the number of the nozzles is 20 to 40.
11. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 9, wherein the aperture of the nozzle is 0.8-2.0 mm.
12. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 9, wherein the distance between any two adjacent nozzles is 5-20 mm.
13. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 1, wherein the cooling speed of the aluminum alloy molten pool is 380-400 ℃/s.
14. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 1, wherein the preset time is the interval time of high-pressure intermittent action on the high-temperature melt.
15. The method for liquid assembly preparation of high-strength and high-toughness aluminum alloy and the composite material thereof in claim 14, wherein the time of the pressure acting on the high-temperature melt is adjusted by the time required for the molten pool of the aluminum alloy to form a semi-solid state area after the high-temperature melt impacts on the surface of the precast block.
16. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 14, wherein the track of the three-dimensional motion of the precast block is serpentine, and the motion speed is 100-150 mm/s.
17. The liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 1, wherein the chemical composition of the high-temperature melt is the same as or different from that of the precast block.
18. The method for liquid assembly preparation of high strength and toughness aluminum alloy and composite material thereof of claim 17, wherein when the chemical composition of the high temperature melt is different from that of the precast block, the chemical composition of the high temperature melt further comprises a reinforcement.
19. The method for preparing the liquid assembly of the high-strength and high-toughness aluminum alloy and the composite material thereof in claim 18, wherein the reinforcement comprises one or more of lithium oxide, aluminum oxide, silicon carbide, silicon nitride, boron carbide, titanium boride, aluminum borate and short fiber reinforcement.
20. The high-strength and high-toughness aluminum alloy and the composite material thereof are characterized by being prepared by adopting the liquid assembly preparation method of the high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in any one of claims 1 to 19.
21. The high-strength and high-toughness aluminum alloy and the composite material thereof as claimed in claim 20, wherein the high-strength and high-toughness aluminum alloy and the composite material thereof are Al-Cu-Mg or Al-Zn-Mg-Cu alloy system.
22. The use of the high-toughness aluminum alloy and the composite material thereof as claimed in claim 20 in the aerospace or military field.
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| CN110125411A (en) * | 2019-06-14 | 2019-08-16 | 上海交通大学 | The preparation facilities and method of melt microcell impact type congruence axialite ingot casting |
| CN111441006A (en) * | 2020-04-22 | 2020-07-24 | 北京科技大学 | Metal structure refining method based on metal liquid flow impact |
| CN111515399A (en) * | 2020-05-15 | 2020-08-11 | 西安交通大学 | Melting, stacking and additive manufacturing method for ceramic particle reinforced metal matrix composite material |
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| CN109202084A (en) * | 2018-11-16 | 2019-01-15 | 上海交通大学 | Array injecting type large scale congruence axialite aluminium alloy ingots increasing material manufacturing equipment and method |
| CN110125411A (en) * | 2019-06-14 | 2019-08-16 | 上海交通大学 | The preparation facilities and method of melt microcell impact type congruence axialite ingot casting |
| CN111441006A (en) * | 2020-04-22 | 2020-07-24 | 北京科技大学 | Metal structure refining method based on metal liquid flow impact |
| CN111515399A (en) * | 2020-05-15 | 2020-08-11 | 西安交通大学 | Melting, stacking and additive manufacturing method for ceramic particle reinforced metal matrix composite material |
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