CN113881873B - High-density trans-scale solid solution ceramic reinforced aluminum matrix composite and preparation method thereof - Google Patents
High-density trans-scale solid solution ceramic reinforced aluminum matrix composite and preparation method thereof Download PDFInfo
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Abstract
The invention discloses a high-density cross-scale solid solution ceramic reinforced aluminum matrix composite material and a preparation method thereof, wherein the high-density cross-scale solid solution ceramic reinforced aluminum matrix composite material comprises an aluminum matrix, and a TiC ceramic reinforcing phase and a ZrC ceramic reinforcing phase which are dispersed in the aluminum matrix; the TiC ceramic reinforcing phase accounts for 4-8 wt% of the total mass of the composite material; the ZrC ceramic reinforcing phase accounts for 6-12 wt% of the total mass of the composite material. In the invention, the ZrC and TiC ceramic reinforcing phase is added into the aluminum matrix, and the ZrC and TiC reinforcing phase are subjected to solid solution in the laser forming process to generate a high-density cross-scale (Ti, zr) C solid solution, so that the reinforcing effect of the solid solutions with different sizes is exerted, and the effect of improving the mechanical property of the material is finally played.
Description
Technical Field
The invention belongs to the field of ceramic reinforced aluminum matrix composites, and particularly relates to a high-density cross-scale solid solution ceramic reinforced aluminum matrix composite and a preparation method thereof.
Background
The aluminum matrix composite material is widely introduced in the fields of aerospace, electronics, chemistry and the like due to the characteristics of low density, high specific strength, high specific modulus, good wear resistance, corrosion resistance, strong designability and the like. By selecting a proper reinforcing phase, the aluminum matrix composite material can obtain higher strength and elastic modulus than the matrix material. Research shows that the strength of the material can be improved and the original ductility can be maintained by adding the nano reinforcing phase. However, strong van der waals force exists among the nanoparticles, and agglomeration is easy to occur, so that high-content nanoparticles are difficult to uniformly disperse in a matrix, and the forming quality and performance of the material are affected finally. Therefore, when the nano reinforcing phase is adopted, the addition amount of the reinforcing phase is limited, the performance improvement space of the final composite material is limited, and the engineering application of the nano particle reinforced aluminum-based composite material is limited.
Disclosure of Invention
The purpose of the invention is as follows: the invention aims to solve the technical problem of the prior art and provides a high-density cross-scale solid solution ceramic reinforced aluminum matrix composite material so as to exert the strengthening effect of solid solutions with different sizes and improve the mechanical property of the material.
In order to achieve the purpose, the technical scheme adopted by the invention is as follows:
a high-density cross-scale solid solution ceramic reinforced aluminum matrix composite comprises an aluminum matrix, and a TiC ceramic reinforcing phase and a ZrC ceramic reinforcing phase which are dispersed in the aluminum matrix;
wherein, the TiC ceramic reinforcing phase accounts for 4 to 8 weight percent of the total mass of the composite material;
the ZrC ceramic reinforcing phase accounts for 6-12 wt% of the total mass of the composite material.
Further, the mass fraction ratio of the TiC ceramic reinforcing phase to the ZrC ceramic reinforcing phase is 2:3.
Preferably, the aluminum matrix is pure Al, or an Al-Mg alloy.
Further, the invention also provides a preparation method of the high-density cross-scale solid solution ceramic reinforced aluminum matrix composite, which comprises the following steps:
(1) Taking matrix powder, tiC ceramic powder and ZrC ceramic powder, and carrying out ball milling and mixing uniformly under the protection of inert gas by a ball mill to obtain composite powder;
(2) Building a three-dimensional entity geometric model of the part by using Soildworks software, then carrying out layered slicing on the model by using Magics software and planning a laser scanning path, dispersing the three-dimensional entity into a series of two-dimensional data, storing and guiding the two-dimensional data into selective laser melting forming equipment;
(3) And (3) melting and solidifying the composite powder in the step (1) layer by the selective laser melting and forming equipment according to the data imported in the step (2), and finally forming the target three-dimensional solid part.
Preferably, in the step (1), when the matrix is pure Al, the purity is not lower than 99.9%, and the particle size distribution range in the matrix powder is 15-53 μm; when the matrix is Al-Mg alloy, the Mg content is not higher than 4.5wt.%, and the particle size distribution range of the matrix powder is 25-60 μm.
Preferably, in the step (1), the grain size distribution range of the TiC ceramic powder is 2-4 μm, and the purity is not lower than 99%.
Preferably, in the step (1), the ZrC ceramic powder has the particle size distribution range of 2-5 μm and the purity of not less than 99.8%.
Preferably, in the step (1), the ball mill adopts a QM series planetary ball mill, the ball-to-material ratio is 2:1, the ball milling rotating speed is 150-250 rpm, and the ball milling time is 3-5 h. And (3) preventing the temperature in the ball milling tank from being overhigh due to overlong continuous ball milling time, and adopting a one-way interval operation mode, namely operating for 15min and standing for 5min. The ball milling process requires that it be conducted under inert gas shielding to prevent oxidation or contamination of the aluminum-based powder during the ball milling process.
Preferably, in the step (3), SLM-150 type selective laser melting equipment is used, and the equipment mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, the aluminum alloy substrate subjected to sand blasting treatment is fixed on a selective laser melting forming equipment workbench and leveled, and then a forming cavity is sealed through a sealing device, vacuumized and introduced with inert gas protective atmosphere. A typical selective laser fusion forming process is as follows: (a) Uniformly laying the powder to be processed on a forming substrate by a powder laying device, scanning the slice area layer by a laser beam according to a pre-designed scanning path, and rapidly melting/solidifying a powder layer so as to obtain a first two-dimensional plane of the part to be formed; (b) The computer control system enables the forming substrate to descend by the thickness of a powder layer, the piston of the powder supply cylinder ascends by the thickness of a certain powder layer, the powder laying device lays a layer of powder to be processed again, and the high-energy laser beam finishes scanning of a second layer of powder according to the slice information to obtain a second two-dimensional plane of the part to be formed; (c) And (c) repeating the step (b), and forming the powder to be processed layer by layer until the part to be formed is processed.
Preferably, the laser power adopted by the selective laser melting forming equipment is 375-425W, the laser scanning speed is 800-1200 mm/s, the scanning interval is 60 mu m, the powder spreading thickness is 30 mu m, a subarea island scanning strategy is adopted, and the laser parameters are determined after process optimization. The aluminum matrix composite reinforcing phase can be reasonably selected and properly added according to the structure and performance characteristics of the aluminum matrix composite, and the preparation method combined with the front-edge selective laser melting technology is adopted, so that the appearance, size and distribution state of the ceramic reinforcing phase can be effectively adjusted, and the aluminum matrix composite with good forming quality and excellent comprehensive performance can be successfully prepared.
Has the beneficial effects that:
1. when the TiC and ZrC ceramic particle reinforced aluminum matrix composite material is irradiated by laser to be melted to form a molten pool, the micron TiC and ZrC reinforced phases are partially melted, and Ti atoms and Zr atoms in the TiC and ZrC ceramic particles are substituted by each other in any proportion due to the diffusion of Ti, zr and C elements to form a micron-scale and submicron-scale (Ti, zr) C solid solution. The fine ceramic particles are completely melted and decomposed into Ti, zr, and C atoms. When the temperature is higher than 2000 ℃, ti, zr and C elements form a completely single (Ti, zr) C solid solution, are separated out in the form of a nano-scale (Ti, zr) C solid solution in the subsequent rapid solidification process, and are dispersed in the Al matrix, and finally a synergistic effect of cross-scale solid solution ceramic reinforcement is formed to improve the mechanical property of the Al matrix. According to the invention, through the interaction of ZrC and TiC at high temperature, a (Ti, zr) C solid solution with cross-scale high-density distribution is formed in the matrix, the nano-scale (Zr, ti) C is dispersed and distributed in the matrix to play a role in hindering dislocation movement, the uniformly distributed micron and submicron-scale (Zr, ti) C solid solution plays a role in second phase strengthening, the (Ti, zr) C solid solutions with different sizes play a role in cooperative strengthening, and the forming quality and performance of the aluminum-based composite material are improved.
2. In the present invention, the aluminum matrix is dispersed in the aluminum matrixThe micron TiC ceramic reinforcing phase and the ZrC ceramic reinforcing phase in the composite powder are used as raw materials, the powder is mixed and then placed in a QM series planetary ball mill for ball milling and powder mixing, and the composite powder which is uniform in ceramic reinforcing phase distribution, good in flowing performance, high in laser absorption rate, suitable for selective laser melting forming and simple and cost-saving is finally obtained through a ball milling process. The selective laser melting technology is adopted to prepare the ceramic reinforced aluminum matrix composite material, so that the production period is shortened, the production efficiency of products is improved, and parts with complex geometric shapes can be formed almost without subsequent machining treatment. The cooling speed of the molten pool is extremely high and can reach 10 when the selective laser melting forming is carried out 3 ～10 8 K/s, effectively avoiding the agglomeration of nano particles in the traditional processing technology and improving the mechanical property of the part.
3. The laser energy density can be adjusted by changing the laser power and the laser scanning speed, the thermodynamic and dynamic characteristics of a molten pool formed by the action of laser and a powder bed are changed along with the change of the laser energy input of the powder bed, and the generation of metallurgical defects such as spheroidization effect, pores and the like is reduced by reasonably selecting laser process parameters and adjusting the laser energy input, so that the high-density cross-scale solid solution ceramic reinforced aluminum-based composite material with high forming quality is obtained.
Drawings
The foregoing and/or other advantages of the invention will become further apparent from the following detailed description of the invention when taken in conjunction with the accompanying drawings.
FIG. 1 is an SEM image of a cross-scale (Ti, zr) C reinforced aluminum matrix composite specimen prepared in example 1.
FIG. 2 is a schematic representation of a trans-scale reinforcing phase in a trans-scale (Ti, zr) C reinforced aluminum matrix composite specimen prepared in example 1.
FIG. 3 is an SEM image of a cross-scale (Ti, zr) C reinforced aluminum matrix composite specimen prepared in example 2.
Fig. 4 is an optical image of a sample of pure aluminum material prepared in comparative example 1.
FIG. 5 is an SEM image of a ZrC reinforced Al matrix composite specimen prepared in comparative example 2.
Detailed Description
The invention will be better understood from the following examples.
In the following examples, pure aluminum base powders having a particle size distribution in the range of 15 to 53 μm and a purity of not less than 99.9% were used, al-Mg alloy powders having a particle size distribution in the range of 25 to 60 μm and a Mg content of not more than 4.5wt.%.
The grain size distribution range of the used TiC ceramic powder is 2-4 mu m, and the purity is not lower than 99%.
The grain size distribution range of the ZrC ceramic powder is 2-5 mu m, and the purity is not lower than 99.8%.
Example 1
(1) ZrC ceramic powder and TiC ceramic powder are mixed with pure Al powder according to the proportion of 3:2, the mass of the ceramic powder accounts for 20% of the total mass of the composite powder, and the cross-scale (Ti, zr) C reinforced aluminum-based composite powder is prepared by ball milling mixed powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a ceramic tank is adopted in the process, and the ball milling media are ceramic grinding balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling rotating speed is 200rpm, and the ball milling time is 4 hours. Meanwhile, the over-high temperature in the ball milling tank due to the overlong continuous ball milling time is prevented, and the equipment operation mode during ball milling adopts a one-way interval operation mode, namely, operation is carried out for 15min, and standing is carried out for 5min. The ball milling process requires that it be conducted under argon protection to prevent oxidation or contamination of the aluminum-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the data and guiding the data into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 425W, the laser scanning speed is 1200mm/s, the scanning interval is 60 mu m, the powder spreading thickness is 30 mu m, a subarea island-shaped scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the ZrC and TiC ceramic reinforced aluminum-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, fixing the aluminum alloy substrate subjected to sand blasting treatment on a selective laser melting forming equipment workbench, leveling, sealing a forming cavity through a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30 mbar) to ensure O in a forming chamber 2 The content is less than 10ppm. A typical selective laser fusion forming process is as follows: (a) Uniformly laying the powder to be processed on a forming substrate by a powder laying device, scanning a slicing area line by a laser beam according to a pre-designed scanning path, and rapidly melting and solidifying a powder layer to obtain a first two-dimensional plane of a part; (b) The computer control system enables the forming substrate to descend by one powder layer thickness, conversely, enables the powder supply cylinder piston to ascend by a certain powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam completes scanning of a second powder layer according to the slicing information to obtain a second two-dimensional plane of the part; (c) And (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
(4) And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the trans-scale (Ti, zr) C reinforced aluminum matrix composite three-dimensional solid part. And (4) grinding, polishing and corroding the composite material block sample according to a standard metallographic sample preparation method. The cross-scale (Ti, zr) C reinforced aluminum matrix composite sample prepared in the selective laser melting process has no generation of pores, and reinforced particles are uniformly distributed in a matrix. SEM analysis was performed on the sample prepared in example 1, see fig. 1. As can be seen from the figure, the (Ti, zr) C solid solution reinforcing phase exists in the material in the form of micron, submicron and nanometer, and the formed cross-scale (Ti, zr) C reinforcing phase is schematically shown in fig. 2. This indicates that during the selective laser melting forming process, zrC and TiC undergo a solid solution reaction to form a solid solution reinforcing phase across the scale in the aluminum matrix.
The tensile strength of the obtained trans-scale (Ti, zr) C reinforced aluminum matrix composite sample can reach 307.8MPa, is 3.28 times of that of pure aluminum (the tensile strength of the pure aluminum is 94 MPa), and has higher strength.
Example 2
(1) ZrC ceramic powder and TiC ceramic powder are mixed with pure aluminum metal powder according to the proportion of 3:2, the mass of the ceramic powder accounts for 15% of the total mass of the composite powder, and the cross-scale (Ti, zr) C reinforced aluminum-based composite powder is prepared by ball milling mixed powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a ceramic tank is adopted in the process, and the ball milling media are ceramic grinding balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling rotating speed is 150rpm, and the ball milling time is 5h. Meanwhile, the over-high temperature in the ball milling tank due to the overlong continuous ball milling time is prevented, and the equipment operation mode during ball milling adopts a one-way interval operation mode, namely, operation is carried out for 15min, and standing is carried out for 5min. The ball milling process requires that it be conducted under argon protection to prevent oxidation or contamination of the aluminum-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out hierarchical slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the data and guiding the data into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 400W, the laser scanning speed is 1000mm/s, the scanning interval is 60 mu m, the powder spreading thickness is 30 mu m, a subarea island-shaped scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the ZrC and TiC ceramic reinforced aluminum-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder spreading system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Blasting sand before formingFixing the treated aluminum alloy substrate on a selective laser melting forming equipment workbench, leveling, sealing a forming cavity by a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30 mbar) to ensure O in a forming chamber 2 The content is less than 10ppm. A typical selective laser fusion forming process is as follows: (a) The powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) The computer control system enables the forming substrate to descend by one powder layer thickness, conversely, enables the powder supply cylinder piston to ascend by a certain powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam completes scanning of a second powder layer according to the slicing information to obtain a second two-dimensional plane of the part; (c) And (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
(4) And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the trans-scale (Ti, zr) C reinforced aluminum matrix composite three-dimensional solid part. And (3) grinding, polishing and corroding the complex-phase reinforced aluminum-based composite material block sample according to a standard metallographic sample preparation method. The compactness of the trans-scale (Ti, zr) C reinforced aluminum matrix composite sample prepared in the selective laser melting process is higher, the (Ti, zr) C solid solution reinforcing phase is uniformly distributed in the matrix and the content is reduced, and an SEM image of a microstructure is shown in figure 3.
The obtained trans-scale (Ti, zr) C reinforced aluminum matrix composite sample is subjected to room temperature tensile test, and the tensile strength of the sample can reach 299MPa, which is 3.18 times of that of pure aluminum (the tensile strength of the pure aluminum is 94 MPa).
Example 3
(1) Mixing ZrC ceramic powder and TiC ceramic powder with Al-Mg alloy powder according to the proportion of 3:2, wherein the mass of the ceramic powder accounts for 10% of the total mass of the composite powder, and preparing the cross-scale (Ti, zr) C reinforced aluminum-based composite powder by ball milling mixed powder. The ball milling and powder mixing operation is carried out in a QM series planetary ball mill, a ceramic pot is adopted in the process, and ball milling media are ceramic grinding balls with the diameters of 6mm, 8mm and 10 mm. The ball milling process parameters are set as follows: the ball-material ratio is 2:1, the ball milling rotating speed is 250rpm, and the ball milling time is 3h. Meanwhile, the over-high temperature in the ball milling tank due to the over-long continuous ball milling time is prevented, and the equipment operation mode during ball milling adopts a one-way interval operation mode, namely, operation is carried out for 15min, and standing is carried out for 5min. The ball milling process requires that it be conducted under argon gas protection to prevent oxidation or contamination of the aluminum-based powder during the ball milling process.
(2) Target part modeling and slicing process
The method comprises the steps of establishing a three-dimensional solid geometric model of a target part in a computer by using Soildworks software, then carrying out layered slicing and scanning path planning on the three-dimensional solid model by using Magics software, dispersing the three-dimensional solid into a series of two-dimensional data, storing the data and guiding the data into selective laser melting forming equipment. Wherein the laser process parameters are set as follows: the laser power is 375W, the laser scanning speed is 800mm/s, the scanning interval is 60 μm, the powder spreading thickness is 30 μm, a subarea island scanning strategy is adopted, and the rotation angle of the laser scanning direction of the adjacent layer is 37 degrees.
(3) Selective laser fusion forming process
And (2) applying the ZrC and TiC ceramic reinforced aluminum-based composite powder prepared in the step (1) to selective laser melting forming. The system mainly comprises a YLR-500 type optical fiber laser, a laser forming chamber, an automatic powder laying system, a protective atmosphere device, a computer control circuit system and a cooling circulation system. Before forming, fixing the aluminum alloy substrate subjected to sand blasting treatment on a selective laser melting forming equipment workbench, leveling, sealing a forming cavity through a sealing device, vacuumizing, and introducing argon protective atmosphere (Ar purity is 99.999%, outlet pressure is 30 mbar) to ensure O in a forming chamber 2 The content is less than 10ppm. A typical selective laser fusion forming process is as follows: (a) The powder spreading device uniformly spreads the powder to be processed on the forming substrate, and the laser beam scans the slice area line by line according to a pre-designed scanning path to rapidly melt and solidify the powder layer, so that a first two-dimensional plane of the part is obtained; (b) The computer control system lowers the formed substrate by one powder layer thickness,conversely, the piston of the powder supply cylinder is lifted by a certain powder layer thickness, the powder laying device re-lays a layer of powder to be processed, and the laser beam finishes scanning a second powder layer according to the slice information to obtain a second two-dimensional plane of the part; (c) And (c) repeating the step (b), and forming the powder to be processed layer by layer until the part is processed.
(4) And after cooling, taking the formed substrate out of the equipment, and separating the part from the substrate by using a linear cutting process to obtain the trans-scale (Ti, zr) C reinforced aluminum matrix composite three-dimensional solid part. And (3) grinding, polishing and corroding the complex-phase reinforced aluminum-based composite material block sample according to a standard metallographic sample preparation method. The composite material sample prepared in the selective laser melting process has no pores, the content of solid solution reinforced phase is reduced, and the solid solution reinforced phase (Ti, zr) C exists in the material in the forms of micron, submicron and nanometer.
The obtained cross-scale (Ti, zr) C reinforced aluminum matrix composite sample is subjected to room temperature tensile test, the tensile strength of the sample can reach 465.4MPa, and is 1.22 times of that of pure Al-Mg alloy (the tensile strength of the pure Al-Mg alloy is 382 MPa).
Comparative example 1
The comparative example is the same as the example 1 except that in the step (1), the ZrC and TiC ceramic powder is not used as the reinforcing phase raw material to prepare the composite powder by ball milling, and the pure aluminum powder is selected to perform selective laser melting forming, and the microstructure of the composite powder is shown in FIG. 4. Comparing fig. 1 and fig. 4, it can be found that after the pure aluminum powder without the ceramic reinforcing phase in comparative example 1 is subjected to selective laser melting forming, a great amount of metallurgical defects such as holes are generated in the forming process due to the reasons of poor powder flowability, low laser absorption rate, easy oxidation and the like, so that the forming quality of the final sample is not high. The tensile strength of the pure aluminum sample prepared in the comparative example 1 is 94MPa, and compared with the cross-scale (Ti, zr) C reinforced aluminum matrix composite material obtained by adding ZrC and TiC ceramics in the example 1, the forming quality and the tensile strength are obviously reduced.
Comparative example 2
The specific procedure of this comparative example is substantially the same as example 1, except that: in the step (1) of the comparative example, single ZrC ceramic powder and pure Al powder are mixed, the mass of the ceramic powder accounts for 20% of the total mass of the composite powder, and the composite powder is prepared by ball milling and powder mixing. In the comparative example, during the selective laser melting forming process, the ZrC ceramic powder is difficult to be fully melted and is unevenly dispersed to form a large number of pores, and meanwhile, the wettability between the ZrC ceramic and the aluminum matrix is poor, so that the interface bonding between the reinforcing phase and the matrix is poor, as shown in fig. 5, and the mechanical property of the ZrC/Al composite material is affected finally. The tensile strength of a single ZrC ceramic powder reinforced pure Al sample is only 175MPa, and compared with the cross-scale (Ti, zr) C reinforced aluminum matrix composite material obtained by adding ZrC and TiC ceramic in example 1, the forming quality and the tensile strength are greatly reduced.
Comparative example 3
The specific procedure of this comparative example is substantially the same as example 1, except that: in the step (1) of the comparative example, pure Al powder of single TiC ceramic powder is mixed, the mass of the ceramic powder accounts for 20% of the total mass of the composite powder, and the composite powder is prepared by ball milling and powder mixing. In the comparative example, in the selective laser melting forming process, tiC ceramic powder is difficult to melt fully and is dispersed unevenly, and meanwhile, the interface bonding between incompletely melted TiC ceramic particles and an Al matrix is poor, so that the forming quality of a sample is poor, and the mechanical property of the TiC/Al composite material is influenced. The tensile strength of the single TiC ceramic powder reinforced pure Al sample is only 203MPa, and compared with the cross-scale (Ti, zr) C reinforced aluminum matrix composite material obtained by adding ZrC and TiC ceramic in the example 1, the tensile strength is greatly reduced.
Comparative example 4
The specific procedure of this comparative example is substantially the same as example 1, except that: in the step (1) of the comparative example, zrC ceramic powder and TiC ceramic powder with the particle size distribution range of 10-20 mu m are mixed with pure Al powder according to the proportion of 3:2, and the composite powder is prepared by ball milling and mixing the ceramic powder accounting for 20% of the total weight of the composite powder. In the comparative example, the original powder particle size was too large, and the reinforcing phase ceramic powder content was too high, so that the ceramic powder was difficult to sufficiently melt during the selective laser melting forming process, and the wettability with the aluminum matrix was poor, resulting in poor interface bonding between the reinforcing phase and the matrix. On the other hand, because the composite powder contains large-size polygonal ceramic particles, the powder has poor flowability, the powder is not uniformly spread on the substrate, a large number of metallurgical defects such as pores are generated in the selective laser melting forming process, the large-size ceramic particles still exist in the matrix, and the nano reinforced phase is obviously reduced, compared with the cross-scale (Ti, zr) C reinforced aluminum-based composite material obtained by adding ZrC and TiC ceramics in the embodiment 1, the forming quality and the tensile strength are greatly reduced.
Comparative example 5
The specific procedure of this comparative example is substantially the same as example 1, except that: in the step (1) of the comparative example, zrC ceramic powder and TiC ceramic powder with the particle size distribution range of 40-50 nm are mixed with pure aluminum metal powder according to the proportion of 3:2, and the composite powder is prepared by ball milling and mixing the ceramic powder accounting for 20% of the total weight of the composite powder. In the comparative example, because strong van der waals force exists among original nano powder particles, agglomeration is easy to occur, ball milling cannot enable a ceramic reinforcing phase to be completely and uniformly dispersed in a matrix, more pores are generated in a selective laser melting forming process, and the forming quality of a final sample is poor. The agglomerated ceramic reinforcing phase in the comparative example cannot be fully dissolved in solid, and the solid solution is distributed in a concentrated manner, so that the tensile strength is greatly reduced compared with the cross-scale (Ti, zr) C reinforced aluminum matrix composite material obtained by adding ZrC and TiC ceramic in example 1.
As can be seen from the example 1 and the comparative examples 1 to 5, the pores of the cross-scale (Ti, zr) C reinforced aluminum matrix composite sample formed by the selective laser melting technology are obviously reduced, the forming quality is obviously improved, the reinforced phase is uniformly dispersed, the tensile strength is maintained at a higher level, the mechanical property is optimized and is 1.22 to 3.28 times of the tensile strength of the original aluminum matrix material. The main reason is that in the selective laser melting and forming process, tiC and ZrC particles are melted and subjected to solid solution reaction in an aluminum matrix to form a micron, submicron, nanoscale, cross-scale and high-density (Ti, zr) C solid solution which is uniformly distributed in the matrix. The nano-scale (Zr, ti) C is dispersed in the matrix and can block dislocation movement, the micron and submicron-scale (Zr, ti) C solid solutions are uniformly distributed to play a role in strengthening the second phase, the (Ti, zr) C solid solutions with different sizes play a role in synergistic strengthening, the tendency of cracking of the composite material in the melt rapid condensation process is reduced, and the forming quality and the mechanical property of the aluminum-based composite material are obviously improved.
The invention provides a thought and a method for a high-density cross-scale solid solution ceramic reinforced aluminum matrix composite material and a preparation method thereof, and a plurality of methods and ways for realizing the technical scheme are provided. All the components not specified in the present embodiment can be realized by the prior art.
Claims (3)
1. A high-density cross-scale solid solution ceramic reinforced aluminum matrix composite is characterized by comprising an aluminum matrix, and a TiC ceramic reinforcing phase and a ZrC ceramic reinforcing phase which are dispersed in the aluminum matrix;
wherein the TiC ceramic reinforcing phase accounts for 4 to 8 wt% of the total mass of the composite material;
the ZrC ceramic reinforcing phase accounts for 6 to 12 wt% of the total mass of the composite material;
the mass fraction ratio of the TiC ceramic reinforcing phase to the ZrC ceramic reinforcing phase is 2:3;
the high-density trans-scale solid solution ceramic reinforced aluminum matrix composite is prepared by the following method:
(1) Taking matrix powder, tiC ceramic powder and ZrC ceramic powder, and carrying out ball milling and mixing uniformly under the protection of inert gas by a ball mill to obtain composite powder;
(2) Establishing a three-dimensional entity geometric model of the part by using Soildworks software, then carrying out layered slicing on the model by using Magics software, planning a laser scanning path, dispersing the three-dimensional entity into a series of two-dimensional data, storing and guiding the two-dimensional data into selective laser melting forming equipment;
(3) According to the data imported in the step (2), the selective laser melting forming equipment melts and solidifies the composite powder in the step (1) layer by layer, and finally forms the target three-dimensional solid part;
in the step (1), when the matrix is pure Al, the purity is not lower than 99.9%, and the particle size distribution range in the matrix powder is 15 to 53 mu m; when the matrix is Al-Mg alloy, the content of Mg is not higher than 4.5 wt%, and the particle size distribution range of matrix powder is 25 to 60 mu m;
in the step (1), the grain size distribution range of the TiC ceramic powder is 2~4 mu m, and the purity is not lower than 99 percent;
in the step (1), the particle size distribution range of the ZrC ceramic powder is 2~5 mu m, and the purity is not lower than 99.8%;
in the step (3), the laser power adopted by the selective laser melting forming equipment is 375-425W, the laser scanning speed is 800-1200 mm/s, the scanning interval is 60 mu m, the powder laying thickness is 30 mu m, and a partitioned island-shaped scanning strategy is adopted.
2. The high density, cross-scale, solid solution ceramic reinforced aluminum matrix composite as claimed in claim 1, wherein said aluminum matrix is pure Al or an Al-Mg alloy.
3. The high-density cross-scale solid solution ceramic reinforced aluminum matrix composite material as claimed in claim 1, wherein in the step (1), the ball mill is a QM series planetary ball mill, the ball-to-material ratio is 2:1, the ball milling speed is 150 to 250rpm, and the ball milling time is 3 to 5 hours.
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