CN112195358A - Aluminum-based alloy, aluminum-based composite material, and preparation method and application thereof - Google Patents
Aluminum-based alloy, aluminum-based composite material, and preparation method and application thereof Download PDFInfo
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- CN112195358A CN112195358A CN202011099168.4A CN202011099168A CN112195358A CN 112195358 A CN112195358 A CN 112195358A CN 202011099168 A CN202011099168 A CN 202011099168A CN 112195358 A CN112195358 A CN 112195358A
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/1089—Alloys containing non-metals by partial reduction or decomposition of a solid metal compound
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Abstract
The invention discloses an aluminum-based alloy, an aluminum-based composite material, and a preparation method and application thereof, and belongs to the technical field of advanced metal-based composite material preparation. The preparation of the aluminum-based alloy comprises the following steps: will K2TiF6And KBF4The mixture and the Al melt are mixed and reacted under the condition of first ultrasonic vibration, cooled to 720-750 ℃, and then subjected to second ultrasonic vibration and casting. By introducing ultrasonic vibration in the mixing process and before pouring, the reaction time can be greatly shortened, crystal grains are refined, clusters are broken, particle agglomeration is effectively eliminated, and the dispersion degree of particles is improved. The prepared aluminum-based alloy has high-dispersion-distribution fine-grain in-situ synthesized titanium diboride grains, and the strength and the hardness of the alloy are obviously improved compared with those of matrix metal. The aluminum-based composite material prepared from the aluminum-based alloy, the alloy elements and the Al material also has better strength and hardness. The aluminum-based alloy and the aluminum-based composite material can be used for producingAerospace devices, automotive manufacturing devices, and the like.
Description
Technical Field
The invention relates to the technical field of advanced metal matrix composite material preparation, and particularly relates to an aluminum-based alloy, an aluminum-based composite material, and preparation methods and applications thereof.
Background
The hard ceramic particles have refining and strengthening effects on the aluminum alloy solidification structure, the specific strength, the specific modulus and the high-temperature stability of the alloy can be greatly improved by adding the fine ceramic particles into the matrix, and the alloy has a very wide application prospect in the fields of aerospace, automobile manufacturing, electronic devices, sports equipment and the like.
The traditional liquid phase preparation method of metal matrix composites is to add externally synthesized reinforcements into the molten matrix. However, the surface of the reinforcement is contaminated, which causes inevitable defects such as poor wettability between the reinforcement and the matrix, poor bonding between the reinforcement and the matrix, serious agglomeration of the reinforcement particles, and formation of interface reaction products. The aluminum-based composite material produced by the in-situ authigenic mixed salt method can effectively avoid the problems of poor wettability between the matrix and the reinforcing phase, the grain size of reinforcing phase particles limited by the size of original particles and the like.
However, the mixed salt method is time-consuming and energy-consuming, and the obtained metal matrix composite material is not obviously improved in strength and hardness compared with a base material.
In view of this, the invention is particularly proposed.
Disclosure of Invention
One of the objectives of the present application includes providing a method for preparing an aluminum-based alloy, which can greatly shorten the reaction time between materials, refine crystal grains, break clusters, effectively eliminate the agglomeration of particles during the reaction, and improve the dispersion degree of the particles.
The second purpose of the present application includes providing an aluminum-based alloy prepared by the above preparation method, and the composite material is significantly improved in strength and hardness compared with the base metal.
A further object of the present application consists in providing the use of the above-mentioned aluminum-based alloy, for example for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
The fourth object of the present application includes providing an aluminum-based composite material prepared from the above aluminum-based alloy and Al material and alloying elements.
The fifth purpose of the present application includes providing a method for preparing the aluminum matrix composite material.
An object of the present application consists in providing the use of the above-mentioned aluminium-based composite material, which can also be used for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
The application can be realized as follows:
in a first aspect, an embodiment of the present invention provides a method for preparing an aluminum-based alloy, including the following steps:
will K2TiF6And KBF4The mixture and the Al melt are mixed and reacted under the condition of first ultrasonic vibration, the mixture is cooled to be not lower than 720 ℃ and not higher than 750 ℃ after the reaction is finished, the temperature is kept for 5-10min, and the second ultrasonic vibration and the pouring are sequentially carried out after the temperature is stabilized.
In an alternative embodiment, the first ultrasonic vibration and the second ultrasonic vibration are performed for 3-6min under the condition of 1-1.5 kW.
In an alternative embodiment, K2TiF6And KBF4The mixture of (A) and Al melt react to theoretically generate TiB2The mass ratio of the particles to the aluminum melt is 1-10%.
In an alternative embodiment, the starting material for the Al melt is commercially pure aluminum.
In an alternative embodiment, the temperature of the Al melt is 800-850 ℃.
In an alternative embodiment, K2TiF6And KBF4The mixture of (A) and the Al melt are mixed under the temperature keeping condition of 800-850 ℃.
In an alternative embodiment, K2TiF6And KBF4The mixture of (a) is mixed with the Al melt in portions.
In an alternative embodiment, the ultrasonic probe is immersed within the Al melt for 10-30mm during the first ultrasonic vibration.
In an alternative embodiment, the ultrasonic probe is immersed in the mixed melt after the first ultrasonic vibration for 10-30mm during the second ultrasonic vibration.
In an alternative embodiment, the ultrasonic probes used for the two ultrasonic vibrations are both made of a Ti alloy material.
In an optional embodiment, the mixed melt is cooled to 720-730 ℃, then is subjected to heat preservation for 5-10min, and is subjected to secondary ultrasonic vibration after the temperature is stable.
In an alternative embodiment, K2TiF6And KBF4The preparation of the mixture of (a) comprises: will K2TiF6And KBF4Mixing Ti and B in the molar ratio of 1 to 2-2.5.
In an optional embodiment, the method further comprises mixing the mixed K2TiF6And KBF4And (5) drying.
In an optional embodiment, the drying temperature is 200-300 ℃, and the drying time is greater than or equal to 2 h.
In an alternative embodiment, the casting may be followed by air-cooled solidification.
In a second aspect, the present application also provides an aluminum-based alloy prepared by the preparation method according to any one of the preceding embodiments.
In an alternative embodiment, the average grain size of the aluminum-based alloy is 30-40 μm.
In an alternative embodiment, TiB is in an aluminum-based alloy2Is less than 1 μm, preferably less than 500 nm.
In an alternative embodiment, TiB is in an aluminum-based alloy2The mass fraction of the particles is less than 10%.
In a third aspect, the present application provides the use of an aluminium-based alloy as in the previous embodiments, for example for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
In a fourth aspect, the present application provides an aluminum-based composite material prepared from the above aluminum-based alloy, and an Al material and alloying elements.
In an alternative embodiment, the alloying element comprises at least one of Cu, Si, Mn, Mg, and Zn.
In a fifth aspect, the present application provides a method for preparing the above aluminum matrix composite, comprising the following steps: heating the Al material and the alloy elements to the temperature of 700-800 ℃, remelting the Al material and the alloy elements with the aluminum-based alloy, cooling to the temperature of 720-750 ℃, performing third ultrasonic vibration, and pouring into a mold.
In an alternative embodiment, the third ultrasonic vibration is performed for 3-6min at 1-1.5 kW.
In an alternative embodiment, the ultrasonic probe is immersed within the remelted melt for 10-30mm during the third ultrasonic vibration.
In a sixth aspect, the present application provides the use of an aluminium matrix composite material according to the previous embodiments, for example for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
The beneficial effect of this application includes:
according to the preparation method of the aluminum-based alloy, the first ultrasonic vibration is introduced at the stage of mixing the Al melt and the reinforcement, so that a cavitation effect and a sound flow effect can be generated in the melt, the reaction time is greatly shortened, the reaction efficiency is obviously improved, the energy is saved, and the production efficiency is improved. After the reaction is finished, cooling to a certain temperature, and performing secondary ultrasonic vibration and casting, so that the particle dispersion uniformity is further improved, the formation of non-dendritic structures is promoted, the enhancement effect of olotawny is improved, and meanwhile, fine and dispersed TiB2The particles can also be used as good alpha-Al nucleation sites during solidification, further promote grain refinement, and are beneficial to improving the strength and hardness of the composite material.
The prepared aluminum-based alloy has high-dispersion-distribution fine-grain in-situ synthesized titanium diboride grains, and compared with matrix metal, the composite material is obviously improved in strength and hardness. The aluminum-based alloy is further used for preparing the aluminum-based composite material, and the hardness and the strength of the aluminum-based composite material can be effectively improved.
The aluminum-based alloy and the aluminum-based composite material can be used for producing aerospace devices, automobile manufacturing devices, electronic devices or sports equipment.
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 a 2 wt.% TiB prepared by secondary sonication2Microstructure photos and phase XRD diffraction patterns of the/Al composite material;
FIG. 2 is a schematic diagram of the preparation of in-situ autogenous TiB by introducing stirring and ultrasonic vibration2A microstructure photograph of the particle-reinforced aluminum-based composite material;
FIG. 3 is an in situ autogenous 2 wt.% TiB prepared by two different processes including agitation and secondary ultrasonic vibration2Macroscopic metallography picture of Al-based composite material.
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 conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The aluminum-based alloy and the aluminum-based composite material provided by the present application, and the preparation method and the application thereof are specifically described below.
At present, the particle size of reinforced phase particles synthesized in situ by a mixed salt method is mostly submicron and nanometer, the reinforced phase particles have higher surface energy, and the reinforced phase particles are usually seriously agglomerated in a matrix, so that the strength and the hardness of the composite material are influenced. In the prior art, mechanical stirring is usually introduced during reaction to improve the reaction efficiency and eliminate particle clusters, but the mechanical stirring can only eliminate large clusters, and cannot provide enough shearing force for small clusters to break the clusters, so that the improvement on the reaction efficiency is not obvious, and impurities are easily introduced. The inventor creatively discovers through long-term research and practice that: the ultrasonic vibration is introduced at a specific stage, so that the reaction process can be accelerated, the cleaning and degassing can be realized, the generated cavitation effect and acoustic flow effect generate huge shearing force in the melt, small particle clusters can be effectively crushed, the uniformity of particles in a matrix is improved, the damage of the particle clusters to the performance is avoided, and the strength and the hardness of the composite material can be obviously improved.
Therefore, the present application proposes a method for preparing an aluminum-based alloy, which comprises the following steps:
will K2TiF6And KBF4The mixture and the Al melt are mixed and reacted under the condition of first ultrasonic vibration, the mixture is cooled to be not lower than 720 ℃ and not higher than 750 ℃ after the reaction is finished, and second ultrasonic vibration and casting are sequentially carried out after the temperature is stabilized.
In an alternative embodiment, the first ultrasonic vibration and the second ultrasonic vibration may be performed for 3 to 6min under a condition of 1 to 1.5 kW. That is, the first ultrasonic vibration can be performed for 3-6min under the condition of 1-1.5kW, and the second ultrasonic vibration can also be performed for 3-6min under the condition of 1-1.5 kW. It should be noted that the first ultrasonic vibration and the second ultrasonic vibration are independent processes, and the conditions of the two ultrasonic vibration processes may be the same or different. Specifically, the power of the ultrasonic vibration may be 1kW, 1.1kW, 1.2kW, 1.3kW, 1.4kW, or 1.5kW, and the optimum ultrasonic time may be 3min, 4min, 5min, or 6min, or the like. The reaction can not be completely finished when the ultrasonic time is less than 3min, and the ultrasonic time exceeding 6min has no obvious beneficial effect and is easy to cause excessive loss to the ultrasonic probe.
In an alternative embodiment, K2TiF6And KBF4The mixture of (A) and Al melt react to theoretically generate TiB2The mass ratio of the particles to the aluminum melt is 1-10%.
Wherein, K2TiF6The purity of (B) is preferably not less than 99.5%, KBF4The purity of (B) is preferably not less than 98%.
In an alternative embodiment, the raw material of the Al melt is industrial pure aluminum (the purity is more than or equal to 99.7%), and the Al melt can be industrial pure aluminum cast ingots.
In alternative embodiments, the temperature of the Al melt may be 800-. The reaction efficiency is higher in the temperature range, and the loss of B element and unnecessary hydrogen absorption and oxidation caused by high temperature are avoided.
In an alternative embodiment, K2TiF6And KBF4The mixture is mixed with Al melt under the heat preservation condition of 800-850 ℃, and TiB is generated in situ through the reaction of mixed salt and Al2And (3) granules. For example, the industrial pure aluminum ingot can be heated to 800-2TiF6And KBF4A mixture of (a).
Preferably, K2TiF6And KBF4The mixture of (a) is mixed with the Al melt in batches to avoid excessive temperature fluctuation caused by one-time pouring.
In an alternative embodiment, the ultrasonic probe is immersed in the Al melt for 10-30mm, such as 10mm, 15mm, 20mm, 25mm, or 30mm, during the first ultrasonic vibration. The ultrasonic power temperature in the range can avoid the reduction of the ultrasonic power and the unnecessary loss of the ultrasonic probe caused by excessive probe immersion.
After the first ultrasonic vibration, the method can also comprise removing the redundant fluorine salt on the surface of the reacted material.
On the basis, the first ultrasonic vibration is introduced at the stage of mixing the Al melt and the reinforcement, so that the cavitation effect and the acoustic flow effect can be generated in the melt, the reaction time is greatly shortened, the reaction efficiency is obviously improved, the energy is saved, and the production efficiency is improved. Specifically, taking the same effect as an example, mechanical stirring needs more than 60 minutes, and the first ultrasonic vibration of the present application needs only about 5 minutes.
In an alternative embodiment, the ultrasonic probe is immersed in the mixed melt (i.e., K) after the first ultrasonic vibration during the second ultrasonic vibration2TiF6And KBF4Mixture of (2) with Al meltInner 10-30mm, such as 10mm, 15mm, 20mm, 25mm or 30 mm. The ultrasonic power temperature in the range can avoid the reduction of the ultrasonic power and the unnecessary loss of the ultrasonic probe caused by the excessive probe immersion.
In an alternative embodiment, the ultrasonic probe used for the two ultrasonic vibrations can be made of a Ti alloy material.
In an optional embodiment, the mixed melt is cooled to 720-730 ℃ (such as 720 ℃, 725 ℃ or 730 ℃), then is subjected to heat preservation for 5-10min, is subjected to secondary ultrasonic vibration after the temperature is stabilized, is subjected to heat preservation for 5-10min, and is poured after the temperature is stabilized, so that air holes caused by overhigh pouring temperature are avoided. The cooling may be accomplished by furnace cooling. Pouring means that the mixed melt after reaction is poured into a preheated mould. The mold may be preheated 2h before casting, the preheating temperature may be 180-. Preferably, the mixed melt is cooled and then is subjected to heat preservation for 5-10min, secondary ultrasonic vibration is carried out after the temperature is stable, and casting can be carried out immediately after the ultrasonic vibration is finished so as to ensure that casting is carried out at the optimal casting temperature.
The secondary ultrasonic vibration is introduced before the pouring, so that the grains can be further refined, clusters can be broken, the particle agglomeration is effectively eliminated, the particle dispersion uniformity and the dispersion degree are improved, the formation of non-dendritic crystal structures is promoted, the Olympic strengthening effect is improved, and meanwhile, fine and dispersed TiB2The particles can also be used as good alpha-Al nucleation sites during solidification, further promote grain refinement, and are beneficial to improving the strength and hardness of the composite material.
Preferably, the method further comprises removing scum on the surface of the mixed melt after the second ultrasonic vibration before pouring the mixed melt into the mold.
Referably, K in this application2TiF6And KBF4The preparation of the mixture of (a) may comprise: will K2TiF6And KBF4Mixing at a molar ratio of Ti to B of 1:2-2.5 (such as 1:2, 1:2.1, 1:2.2, 1:2.3, 1:2.4 or 1: 2.5). The mixing means may be mechanical mixing.
Further, the method also comprises mixing the K2TiF6And KBF4Is dried。
In alternative embodiments, the drying temperature may be 200-300 deg.C, such as 200 deg.C, 220 deg.C, 250 deg.C, 280 deg.C or 300 deg.C. The drying time may be, for example, greater than or equal to 2 hours.
Further, the preparation of the aluminum-based alloy further comprises: and performing air cooling solidification after casting.
The aluminum-based alloy prepared by the method has high-dispersion-distribution fine-grain in-situ synthesized titanium diboride grains, and compared with matrix metal, the composite material is obviously improved in strength and hardness.
In some embodiments, the aluminum-based alloys provided herein have an average grain size of 30 to 40 μm.
In some embodiments, TiB in the aluminum-based alloy2Is less than 1 μm, more preferably less than 500 nm.
In some embodiments, TiB in the aluminum-based alloy2The mass fraction of the particles is less than 10%.
In summary, the grain size of the casting blank obtained by the preparation method provided by the application is greatly reduced compared with that of the traditional stirring casting, when a mechanical stirring auxiliary mixed salt reaction process is adopted, the melt temperature needs to be higher than 850 ℃, the reaction time is usually more than 60 minutes, and the obtained TiB2The particle size is submicron and micron, and the particle agglomeration is serious. By adopting the ultrasonic vibration casting process, the reaction time is shortened to 5 minutes, the particle clusters are removed, the final average grain size of the obtained material is 30-40 mu m, and the obtained material is only 30-40 percent of that of the material cast by mechanical stirring and TiB2The particle size is mostly nano-scale, the tensile strength and the hardness of the material are improved in different degrees, and better comprehensive mechanical properties are shown.
The present application also provides the use of the aluminum-based alloy obtained as described above, for example for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
Further, the application also provides an aluminum-based composite material, which is prepared from the aluminum-based alloy, the Al material and alloy elements. The above aluminum-based alloys can be considered as master alloys.
In alternative embodiments, the alloying elements may include, but are not limited to, at least one of Cu, Si, Mn, Mg, and Zn. Different TiB can be manufactured by blending the proportion2Aluminum matrix composite material.
The preparation method of the aluminum matrix composite material comprises the following steps: heating Al material and alloy elements to 700-800 ℃, remelting the Al material and the alloy elements with the aluminum-based alloy, cooling to 720-750 ℃, performing third ultrasonic vibration for 2-5min, and casting into a mold.
In an alternative embodiment, the third ultrasonic vibration may be performed for 3-6min under the condition of 1-1.5 kW. In the third ultrasonic vibration process, the ultrasonic probe is immersed into the melt after remelting by 10-30 mm.
The above process can further improve the strength and hardness of the aluminum matrix composite material.
The aluminum matrix composite material can also be used for producing aerospace devices, automobile manufacturing devices, electronic devices or sports equipment.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
Step 1: will theoretically produce 2 wt.% TiB after reaction with molten Al2K of/Al2TiF6、KBF4Mechanically mixing two kinds of villiaumite according to the molar ratio of Ti to B being 1:2, drying for 2h at the temperature of 250 ℃ after fully mixing, then adding the villiaumite into a pure aluminum melt with the temperature of 830 ℃, simultaneously immersing a Ti alloy ultrasonic probe into the melt with the immersion depth of 20mm, carrying out ultrasonic treatment for 5 minutes and the ultrasonic power of 1.0kW, and obtaining the mixed melt.
Step 2: removing liquid molten salt impurities on the surface of the melt, cooling to 730 ℃, preserving heat for 5min, immersing the ultrasonic probe into the mixed melt again, carrying out ultrasonic treatment for 5min under the condition that the ultrasonic power is 1.0kW, removing surface scum, then pouring into a steel casting die, and naturally cooling to obtain TiB2Al-based alloys of which TiB2The mass percentage is 2%.
The TiB2The microstructure photograph and the phase XRD diffraction pattern of the Al-based alloy are shown in figure 1. Wherein the content of the first and second substances,FIG. 1(a) is the 2 wt.% TiB2Microstructure morphology of/Al-based alloys, FIG. 1(b) is the 2 wt.% TiB2XRD pattern of Al-based alloy, FIG. 1(c) is TiB at grain boundary2The morphology of the particles and the morphology of the clusters are shown in FIG. 1(d) as TiB2And (5) counting the particle size of the particles.
As can be seen from FIG. 1(a), TiB2The particles are uniformly distributed and have no agglomeration phenomenon.
As can be seen from FIG. 1(b), the main component of the material is TiB2And an Al matrix.
As can be seen from FIG. 1(c), most of the TiB2The grain size is fine and mainly exists in the grain boundary.
From FIG. 1(d), TiB can be seen2The grain size of the particles is mainly concentrated at 200-600 nm.
Example 2
Step 1: will theoretically produce 5 wt.% TiB after reaction with molten Al2K of/Al2TiF6、KBF4Mechanically mixing two kinds of villiaumite according to the molar ratio of Ti to B being 1:2, drying for 2h at the temperature of 250 ℃ after fully mixing, then adding the villiaumite into a pure aluminum melt with the temperature of 830 ℃, simultaneously immersing a Ti alloy ultrasonic probe into the melt with the immersion depth of 20mm, carrying out ultrasonic treatment for 5 minutes and the ultrasonic power of 1.0kW, and obtaining the mixed melt.
Step 2: removing liquid molten salt impurities on the surface of the melt, cooling to 730 ℃, preserving heat for 5min, immersing the ultrasonic probe into the mixed melt again, carrying out ultrasonic treatment for 5min under the condition that the ultrasonic power is 1.0kW, removing surface scum, then pouring into a steel casting die, and naturally cooling to obtain TiB2Al-based alloys, TiB2The mass percentage is 5%.
Example 3
Step 1: will theoretically produce 8 wt.% TiB after reaction with molten Al2K of/Al2TiF6、KBF4Mechanically mixing two kinds of villiaumite according to the molar ratio of Ti to B of 1:2, fully mixing, drying for 2h at 250 ℃, adding into a pure aluminum melt with the temperature of 830 ℃, simultaneously immersing a Ti alloy ultrasonic probe into the melt with the immersion depth of 20mm, and carrying out ultrasonic treatment5 minutes, the ultrasonic power is 1.0kW, and a mixed melt is obtained.
Step 2: removing liquid molten salt impurities on the surface of the melt, cooling to 730 ℃, preserving heat for 5min, immersing the ultrasonic probe into the mixed melt again, carrying out ultrasonic treatment for 5min under the condition that the ultrasonic power is 1.0kW, removing surface scum, casting into a steel mould, and naturally cooling to obtain TiB2Al-based alloys, TiB2The mass percentage is 8%.
Example 4
Step 1: will theoretically produce 8 wt.% TiB after reaction with molten Al2K of/Al2TiF6、KBF4Mixing two kinds of villiaumite according to the molar ratio of Ti to B being 1:2, drying for 2h at the temperature of 250 ℃ after fully mixing, then adding the mixture into a pure aluminum melt with the temperature of 830 ℃, simultaneously immersing a Ti alloy ultrasonic probe into the melt with the immersion depth of 20mm, carrying out ultrasonic treatment for 5 minutes and the ultrasonic power of 1.0kW, and obtaining the mixed melt.
Step 2: removing liquid molten salt impurities on the surface of the melt, cooling to 730 ℃, preserving heat for 5min, immersing the ultrasonic amplitude rod into the mixed melt again, carrying out ultrasonic treatment for 5min under the condition that the ultrasonic power is 1.0kW, removing surface scum, casting into a steel mould, and naturally cooling to obtain TiB2Al master alloy, TiB2The mass percentage is 8%.
And step 3: 8 wt.% TiB obtained above2Preparing TiB by using/Al intermediate alloy as raw material2The Al-Cu aluminum matrix composite material specifically comprises the following components: pure Al, Cu, Mg and Zn are used as raw materials, the raw materials are melted and heated to 800 ℃, and 8 wt.% of TiB prepared in the step 2 is added2a/Al master alloy.
And 4, step 4: removing liquid impurities on the surface of the melt, cooling to 730 ℃, immersing the ultrasonic probe into the remelted melt again, immersing the melt into the melt with the depth of 20mm, carrying out ultrasonic treatment for 5 minutes under the condition that the ultrasonic power is 1.0kW, then casting the melt into a steel die, and naturally cooling to obtain TiB2Al-Cu aluminum matrix composite.
Comparative example
A comparative example was set up, and the two sonications in example 1 were performedThe vibration is replaced by mechanical stirring under the condition of 100r/min, and the obtained TiB2TiB in Al-base alloy2The mass percent is also 2 percent, the TiB2The microstructure photograph of the Al-based alloy is shown in FIG. 2(a), and the macro metallographic photograph is shown in FIG. 3 (a). TiB in example 12The microstructure photograph of the Al-based alloy is shown in FIG. 2(b), and the macro metallographic photograph is shown in FIG. 3 (b).
Comparing fig. 2(a) with fig. 2(b) can be seen: under the mechanical stirring process, a large amount of particle agglomeration exists in the matrix, and the agglomeration size is large. The microstructure under the ultrasonic vibration process is more uniform without obvious agglomeration.
Comparing fig. 3(a) with fig. 3(b) can be seen: the crystal grains of the composite material manufactured by the two processes are isometric crystals, the crystal grains are mainly isometric crystals, and the size of the crystal grains of the composite material manufactured by the ultrasonic vibration process is obviously smaller than that of the crystal grains of the composite material manufactured by the mechanical stirring process.
In summary, the preparation method provided by the application is simple and reasonable, and the TiB can be self-generated in situ2During the casting process of the/Al composite material, the reaction temperature is controlled, ultrasonic vibration is introduced to replace the traditional mechanical stirring, grains are obviously refined, and TiB is further improved through secondary ultrasonic vibration2The dispersibility of the particles in an aluminum matrix obviously improves the mechanical property. Has lower economic cost and better industrial popularization, and has stronger competitiveness in technology and economy.
The above is only a preferred embodiment of the present invention, and is not intended to limit the present invention, and various modifications and changes will occur to 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 (10)
1. The preparation method of the aluminum-based alloy is characterized by comprising the following steps of:
will K2TiF6And KBF4The mixture of (A) and Al melt in a first ultrasonic vibration barAnd (3) performing mixing reaction under the components, cooling to the temperature of not less than 720 ℃ and not more than 750 ℃ after the reaction is finished, preserving the heat for 5-10min, and performing secondary ultrasonic vibration and pouring in sequence after the temperature is stable.
2. The production method according to claim 1, wherein the first ultrasonic vibration and the second ultrasonic vibration are performed for 3 to 6min under a condition of 1 to 1.5 kW.
3. The method of claim 1, wherein K is2TiF6And said KBF4Is reacted with the Al melt to theoretically generate TiB2The mass ratio of the particles to the Al melt is 1-10%;
preferably, the raw material of the Al melt is industrial pure aluminum;
preferably, the temperature of the Al melt is 800-850 ℃;
preferably, said K2TiF6And said KBF4The mixture is mixed with the Al melt under the heat preservation condition of 800-850 ℃;
preferably, said K2TiF6And said KBF4Is mixed with the Al melt in portions.
4. The preparation method according to claim 3, wherein during the first ultrasonic vibration, an ultrasonic probe is immersed in the Al melt by 10-30 mm;
preferably, in the second ultrasonic vibration process, the ultrasonic probe is immersed in the mixed melt subjected to the first ultrasonic vibration for 10-30 mm;
preferably, the ultrasonic probes used for the two ultrasonic vibrations are made of Ti alloy;
preferably, the mixed melt is cooled to 720-730 ℃, then is subjected to heat preservation for 5-10min, and is subjected to secondary ultrasonic vibration after the temperature is stable.
5. The method of claim 1, wherein K is2TiF6And said KBF4The preparation of the mixture of (a) comprises: the K is added2TiF6And said KBF4Mixing Ti and B in the molar ratio of 1: 2-2.5;
preferably, the method further comprises mixing the K2TiF6And said KBF4Drying is carried out;
preferably, the drying temperature is 200-;
preferably, the step of air-cooling solidification is further included after the casting.
6. An aluminum-based alloy, characterized by being produced by the production method as recited in any one of claims 1 to 5;
preferably, the average grain size of the aluminium-based alloy is 30-40 μm;
preferably, TiB in the aluminum-based alloy2Is less than 1 μm, more preferably less than 500 nm;
preferably, TiB in the aluminum-based alloy2The mass fraction of the particles is less than 10%.
7. Use of an aluminium-based alloy according to claim 6 for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
8. An aluminum-based composite material, characterized by being prepared from the aluminum-based alloy according to claim 6 and Al materials and alloying elements;
preferably, the alloying element comprises at least one of Cu, Si, Mn, Mg and Zn.
9. The method for preparing an aluminum matrix composite according to claim 8, comprising the steps of: heating the Al material and the alloy elements to the temperature of 700-;
preferably, the third ultrasonic vibration is carried out for 3-6min under the condition of 1-1.5 kW;
preferably, in the third ultrasonic vibration process, the ultrasonic probe is immersed in the melt after remelting for 10-30 mm.
10. Use of an aluminium matrix composite according to claim 8 for the production of aerospace devices, automotive manufacturing devices, electronic devices or sports equipment.
Priority Applications (1)
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