An aluminum matrix composite and a method for producing the same

Abstract

The application provides an aluminum matrix composite material and a preparation method thereof, and belongs to the technical field of aluminum matrix composite materials. The Al-Cu-Fe-Ce quasicrystal intermediate alloy is used as a reinforcing phase, the interface area of the composite material is increased, more grain boundary strengthening effects are provided, and the improvement of the mechanical properties of the composite material is facilitated; through solid solution and aging treatment, uniformly distributed beta phases, Al2CuMg phases belonging to the orthorhombic system, beta'' phases and a small amount of beta' precipitated phases can be formed in the aluminum matrix composite material, the morphology, quantity and distribution state of the phases play an extremely important promoting role on the performance of the composite material; the formed beta phases, Al2CuMg phases, beta'' phases and a small amount of beta' precipitated phases are in the form of fine and uniform distribution in the microstructure of the composite material, and the uniform distribution ensures the consistency of the mechanical properties of the material and improves the mechanical properties of the composite material.

Description

Technical Field

[0001] This invention belongs to the field of aluminum-based composite materials technology, specifically relating to an aluminum-based composite material and its preparation method. Background Technology

[0002] Al-Mg-Si series (6000 series) aluminum alloys have excellent strength, elastic modulus and fatigue resistance, as well as good corrosion resistance and formability. They are widely used in aerospace, transportation, automotive, construction, electronic devices and other fields.

[0003] To further improve its mechanical properties, reinforcing phases are often added to prepare particle-reinforced 6061 aluminum matrix composites, such as silicon carbide and aluminum nitride. However, the addition of these reinforcing particles usually presents the following problems:

[0004] Uneven particle distribution: Some particles may be unevenly distributed, and uniform solid solution and aging treatment may not be achieved during heating, resulting in different crystal structures in local areas and large differences in performance.

[0005] Poor bonding between loosely mixed particles and the matrix: Bonding between loosely mixed particles and aluminum-based materials can be problematic, resulting in loose interfacial contact in the composite material. This can easily lead to delamination or loosening between the particles and the matrix. Furthermore, some reinforcing particles require pretreatment to achieve effective bonding with the aluminum-based material; otherwise, the overall performance of the composite material will be affected.

[0006] Particle-matrix reactive growth: Some particles react with the aluminum matrix to form new phase structures, leading to changes in microstructure and properties. Some particles may melt or agglomerate at high temperatures, resulting in unstable microstructure and decreased performance of the composite material.

[0007] The aforementioned problems lead to a decrease in the mechanical properties of aluminum-based composite materials. Therefore, how to improve the mechanical properties of aluminum-based composite materials has become a technical challenge that urgently needs to be solved in this field. Summary of the Invention

[0008] The purpose of this invention is to provide an aluminum-based composite material and its preparation method. The aluminum-based composite material prepared by the method provided by this invention possesses excellent mechanical properties.

[0009] To achieve the above-mentioned objectives, the present invention provides the following technical solution:

[0010] This invention provides a method for preparing an aluminum-based composite material, comprising the following steps:

[0011] (1) The Al-Cu-Fe-Ce quasi-crystalline intermediate alloy was mixed with the matrix material powder and hot-pressed to obtain the composite material;

[0012] (2) The composite material obtained in step (1) is subjected to solution treatment and aging treatment in sequence to obtain aluminum-based composite material.

[0013] Preferably, in step (1), the Al-Cu-Fe-Ce quasicrystalline master alloy is (Al 63 Cu 25 Fe 12 ) 99 Ce1 quasicrystalline master alloy.

[0014] Preferably, in step (1), the Al-Cu-Fe-Ce quasicrystalline master alloy is 5 to 25% of the volume of the matrix material powder.

[0015] Preferably, the Al-Cu-Fe-Ce quasicrystalline intermediate alloy in step (1) has a particle size of 60 μm.

[0016] Preferably, in step (1), the hot pressing sintering temperature is 460-510°C, the hot pressing sintering time is 20-60 min, and the hot pressing sintering pressure is 30 MPa.

[0017] Preferably, the hot pressing sintering temperature is 490–500°C, and the hot pressing sintering time is 30–50 min.

[0018] Preferably, the solution treatment temperature in step (2) is 510-550°C, and the solution treatment holding time is 1 hour.

[0019] Preferably, the solution treatment temperature is 520–530°C.

[0020] Preferably, the aging treatment temperature in step (2) is 170-190°C, and the aging treatment holding time is 2-24 hours.

[0021] The present invention also provides an aluminum-based composite material prepared by the preparation method described in the above technical solution.

[0022] This invention provides a method for preparing an aluminum-based composite material, comprising the following steps: mixing an Al-Cu-Fe-Ce quasicrystalline intermediate alloy with a matrix material powder and hot-pressing and sintering the mixture to obtain a composite material; subjecting the composite material to solution treatment and aging treatment in sequence to obtain an aluminum-based composite material. This invention uses an Al-Cu-Fe-Ce quasicrystalline intermediate alloy as a reinforcing phase, increasing the interfacial area of ​​the composite material and providing more grain boundary strengthening effects. This makes the stress transfer between the reinforcing phase and the matrix more uniform, effectively improving the tensile strength and hardness of the composite material. In addition, this reinforcing phase can absorb and disperse stress concentration, reducing the formation of stress concentration regions, which helps to improve the wear resistance and corrosion resistance of the composite material. Therefore, the quasicrystalline particles have good wettability with the aluminum matrix, enabling them to effectively bond together and form a tight interfacial structure. This excellent interfacial bonding performance is beneficial to the improvement of the mechanical properties of the composite material. Through solution treatment and aging, a uniformly distributed β phase, an orthorhombic Al2CuMg phase, a β″ phase, and a small amount of β′ precipitates can be formed in the aluminum matrix composite material. The morphology, quantity, and distribution of these phases play an extremely important role in promoting the performance of the composite material. The formed β phase, Al2CuMg phase, β″ phase, and a small amount of β′ precipitates all exist in the microstructure of the composite material in a fine and uniform manner. This uniform distribution ensures the consistency of the material's mechanical properties and improves the mechanical properties of the composite material. Experimental results show that the aluminum-based composite material prepared by the preparation method provided in this invention has excellent mechanical properties. Attached Figure Description

[0023] Figure 1 The microstructure of the composite material obtained in step (2) of Example 1;

[0024] Figure 2 The microstructure of the composite material obtained in step (2) of Example 1;

[0025] Figure 3 The microstructure of the composite material obtained in step (2) of Comparative Example 1;

[0026] Figure 4 The microstructure of the composite material obtained in step (2) of Comparative Example 1;

[0027] Figure 5 The image shows the microstructure of the aluminum-based composite material prepared in Example 1.

[0028] Figure 6 The image shows the microstructure of the aluminum-based composite material prepared in Example 2.

[0029] Figure 7 The image shows the microstructure of the aluminum-based composite material prepared in Example 3.

[0030] Figure 8 The image shows the microstructure of the aluminum-based composite material prepared in Example 4.

[0031] Figure 9 The image shows the microstructure of the aluminum-based composite material prepared in Example 5.

[0032] Figure 10 The image shows the microstructure of the aluminum-based composite material prepared in Example 6.

[0033] Figure 11 The Vickers hardness of the aluminum-based composite materials prepared in Examples 1-9 and Comparative Example 2;

[0034] Figure 12 The tensile strength of the aluminum-based composite materials prepared in Examples 1-9 and Comparative Example 2;

[0035] Figure 13 This is a bright-field image of the β phase in the aluminum-based composite material prepared in Example 5;

[0036] Figure 14 Energy dispersive spectroscopy (EDS) analysis of the β phase in the aluminum-based composite material prepared in Example 5;

[0037] Figure 15 The micro-area diffraction pattern of the β phase in the aluminum-based composite material prepared in Example 5;

[0038] Figure 16 Bright-field images of the β′ and β″ phases in the aluminum-based composite material prepared in Example 5;

[0039] Figure 17 for Figure 16 High-resolution topography and Fourier transform of bright-field image in the middle region 1;

[0040] Figure 18 for Figure 16 High-resolution topography and Fourier transform of bright-field image in the middle region 1;

[0041] Figure 19 for Figure 16 High-resolution topography and Fourier transform of bright-field image in the middle region 2;

[0042] Figure 20 This is a bright-field image of the Al2CuMg phase in the aluminum-based composite material prepared in Example 5;

[0043] Figure 21 Selected area electron diffraction pattern of the Al2CuMg phase in the aluminum-based composite material prepared in Example 5;

[0044] Figure 22 The elemental distribution diagram of the aluminum-based composite material prepared in Example 5 is shown below.

[0045] Figure 23 The image shows the Al element distribution in the aluminum-based composite material prepared in Example 5.

[0046] Figure 24 The image shows the Cu element distribution in the aluminum-based composite material prepared in Example 5.

[0047] Figure 25 The image shows the Fe element distribution in the aluminum-based composite material prepared in Example 5.

[0048] Figure 26 The image shows the Ce element distribution in the aluminum-based composite material prepared in Example 5.

[0049] Figure 27 The image shows the Mg element distribution in the aluminum-based composite material prepared in Example 5.

[0050] Figure 28 The image shows the Si element distribution in the aluminum-based composite material prepared in Example 5. Detailed Implementation

[0051] This invention provides a method for preparing an aluminum-based composite material, comprising the following steps:

[0052] (1) The Al-Cu-Fe-Ce quasi-crystalline intermediate alloy was mixed with the matrix material powder and hot-pressed to obtain the composite material;

[0053] (2) The composite material obtained in step (1) is subjected to solution treatment and aging treatment in sequence to obtain aluminum-based composite material.

[0054] This invention does not impose any special restrictions on the source of the raw materials; commercially available products or well-known preparation methods familiar to those skilled in the art can be used.

[0055] This invention involves mixing an Al-Cu-Fe-Ce quasicrystalline master alloy with a matrix material powder and then hot-pressing and sintering the mixture to obtain a composite material. Using the Al-Cu-Fe-Ce quasicrystalline master alloy as a reinforcing phase increases the interfacial area of ​​the composite material and provides greater grain boundary strengthening effect. This results in more uniform stress transfer between the reinforcing phase and the matrix, effectively improving the tensile strength and hardness of the composite material. Furthermore, this reinforcing phase can absorb and disperse stress concentration, reducing the formation of stress concentration regions and contributing to improved wear resistance and corrosion resistance. The quasicrystalline particles exhibit good wettability with the aluminum matrix, enabling them to effectively bond together and form a tight interfacial structure. This excellent interfacial bonding performance is beneficial to improving the mechanical properties of the composite material.

[0056] In this invention, the Al-Cu-Fe-Ce quasicrystalline intermediate alloy is preferably (Al... 63 Cu 25 Fe 12 ) 99 Ce1 quasicrystalline master alloy.

[0057] In this invention, the (Al) 63 Cu 25 Fe 12 ) 99 The preferred method for preparing Ce1 quasicrystalline master alloy is to sequentially melt, rapidly cool, and remelt the alloy raw materials.

[0058] In this invention, the alloy raw materials are preferably subjected to ultrasonic cleaning and drying before use.

[0059] The present invention does not impose any special limitations on the operation of ultrasonic cleaning and drying; any operation known to those skilled in the art can be used.

[0060] This invention does not impose a specific limitation on the amount of the alloy raw material used, according to (Al) 63 Cu 25 Fe 12 ) 99 Ce1 can be used to prepare the ingredients.

[0061] In this invention, the melting is preferably vacuum arc melting; the vacuum degree of the melting is preferably 5×10⁻⁶. -4 Pa; the smelting is preferably carried out under an argon atmosphere; the smelting is preferably carried out under stirring conditions. The smelting under an argon atmosphere in this invention can prevent oxidation; the smelting under stirring conditions can promote the homogenization of the ingot composition.

[0062] The present invention does not impose any special limitations on the temperature and time of the melting process, as long as the raw materials are completely melted.

[0063] The present invention does not impose any special limitations on the rapid cooling operation; any operation known to those skilled in the art can be used.

[0064] In this invention, the number of times the re-flipping and remelting is performed is preferably four. This invention does not impose any particular limitation on the operation of the re-flipping and remelting; any operation well-known to those skilled in the art can be used. The re-flipping and remelting performed in this invention can improve the uniformity of the composition.

[0065] In this invention, the Al-Cu-Fe-Ce quasicrystalline intermediate alloy is preferably subjected to heat treatment, crushing, manual grinding, sieving and ball milling in sequence before use.

[0066] In this invention, the preferred heat treatment temperature is 750°C; the preferred heat treatment holding time is 6 hours; and the preferred cooling method is air cooling. This invention does not impose any special limitations on the air cooling operation; any operation familiar to those skilled in the art can be used. The quasicrystalline intermediate alloy obtained by vacuum arc melting in this invention is a multiphase alloy, in which the content of the quasicrystalline phase is not very high. To obtain an alloy composed entirely of quasicrystalline phases, the quasicrystalline intermediate alloy needs to be heat-treated.

[0067] The present invention does not impose any special limitations on the crushing, manual grinding, sieving and ball milling operations, as long as the particle size of the Al-Cu-Fe-Ce quasicrystalline intermediate alloy is 60μm.

[0068] In this invention, the preferred particle size of the Al-Cu-Fe-Ce quasicrystalline master alloy is 60 μm. By controlling the particle size of the Al-Cu-Fe-Ce quasicrystalline master alloy, this invention makes the bond between the reinforcing phase and the matrix stronger, reduces the likelihood of porosity and other defects within the reinforcing phase, and decreases the probability of diffusion between the reinforcing phase and the matrix, thereby further improving the strength and hardness of the composite material.

[0069] In this invention, the matrix material powder is preferably 6061 aluminum alloy powder; the Al-Cu-Fe-Ce quasicrystalline master alloy is preferably 5-25% of the volume of the matrix material powder, more preferably 10-20%, and even more preferably 15-20%. This invention improves the reinforcing effect by controlling the volume fraction of the Al-Cu-Fe-Ce quasicrystalline master alloy, thereby further improving the mechanical properties of the composite material.

[0070] The present invention does not have any special limitations on the operation of mixing Al-Cu-Fe-Ce quasicrystalline intermediate alloy with matrix material powder; any technical solution for preparing the mixture well known to those skilled in the art can be used.

[0071] In this invention, the temperature of the hot pressing sintering is preferably 460-510°C, more preferably 490-500°C; the time of the hot pressing sintering is preferably 20-60 min, more preferably 30-50 min; and the pressure of the hot pressing sintering is preferably 30 MPa.

[0072] After obtaining the composite material, the present invention performs solution treatment and aging treatment on the composite material in sequence to obtain an aluminum-based composite material.

[0073] In this invention, the solution treatment temperature is preferably 510–550°C, more preferably 520–530°C; the solution treatment holding time is preferably 1 hour; and the solution treatment cooling method is preferably water cooling. This invention does not impose any special limitations on the water cooling operation; any operation well-known to those skilled in the art can be used.

[0074] In this invention, the aging treatment temperature is preferably 170–190°C, more preferably 170–180°C; the aging treatment holding time is preferably 2–24 h, more preferably 5–12 h, and more preferably 10 h; the aging treatment cooling method is preferably air cooling. This invention does not have any special limitations on the air cooling operation; any operation well known to those skilled in the art can be used. This invention, by limiting the process parameters of the aging treatment, can significantly improve the strength and hardness of the composite material; the constituent phases of the aluminum-based composite material include the β phase, the orthorhombic Al2CuMg phase, the β″ phase, and a small amount of β′ precipitates. The constituent phases are fine and uniformly distributed, which plays a significant role in improving the tensile strength and hardness of the composite material.

[0075] This invention, through aging treatment following solution quenching, enables the formation of uniformly distributed β phase, orthorhombic Al2CuMg phase, β″ phase, and a small amount of β′ precipitate in Al-Cu-Fe-Ce quasicrystalline reinforced 6061 aluminum matrix composites. The morphology, quantity, and distribution of these phases play a crucial role in promoting the performance of the composite material. Firstly, the formed β phase, orthorhombic Al2CuMg phase, β″ phase, and a small amount of β′ precipitate exist in the microstructure of the composite material in a fine and uniform manner. This uniform distribution ensures the consistency of the material's mechanical properties and improves the tensile strength and hardness of the composite material. Furthermore, the morphology and quantity of the β phase, orthorhombic Al2CuMg phase, β″ phase, and a small amount of β′ precipitate can be controlled by adjusting the processing technology, thereby achieving precise adjustment of the material's properties.

[0076] This invention introduces an Al-Cu-Fe-Ce quasicrystalline reinforcing phase into an aluminum alloy matrix to create a composite material. The addition of the quasicrystalline intermediate alloy as a reinforcing phase effectively improves the mechanical properties, thermal stability, corrosion resistance, and interfacial bonding strength of the particle-reinforced 6061 aluminum matrix composite, providing broader possibilities for its applications. Simultaneously, it addresses the shortcomings of quasicrystalline particle-reinforced 6061 aluminum matrix composites in age hardening and further develops the age hardening capability of the composite material. The method provided by this invention offers a feasible process route for preparing high-performance aluminum matrix composites. The application of this process is expected to improve the mechanical properties and durability of the composite material, providing a more reliable option for the application of aluminum matrix composites in aerospace, transportation, and other fields.

[0077] The quasicrystalline intermediate alloy used in this invention, as a reinforcing phase, possesses high hardness and strength. Its addition forms a three-dimensional reinforcing network structure in the composite material, acting as a particle reinforcement. The interaction between these quasicrystalline particles and the aluminum matrix enhances the composite material's tensile strength, yield strength, and hardness. Furthermore, due to their diverse geometries, chemical compatibility, interfacial energy matching, and thermal stability, the quasicrystalline particles achieve better uniform distribution within the composite material. This uniform distribution helps improve the overall performance of the composite material and reduces performance differences between different regions. Simultaneously, addressing the issue of weak bonding between loose particles and the matrix, the quasicrystalline particles exhibit high interfacial bonding strength with the aluminum matrix, effectively resisting particle separation and delamination, improving the overall structural strength of the composite material, and contributing to enhanced wear resistance, corrosion resistance, and fatigue resistance. Mutual reactions occur between the quasicrystalline particles and the aluminum matrix, particularly the diffusion between the boundaries of the quasicrystalline particles and the matrix. Some quasicrystalline particles will... The precipitates transform into fine β phases, which enhance the strength and hardness of the composite material and optimize its microstructure, further improving its overall performance. Quasicrystalline particles possess good thermal stability, maintaining their shape and structure during solid-state processing. This thermal stability helps prevent melting or agglomeration during heating, promoting their uniform distribution within the composite material and allowing them to maintain their reinforcing effect while improving the composite's resistance to thermal creep and high-temperature oxidation. Furthermore, the addition of quasicrystalline particles positively impacts the aging precipitates in quasicrystalline particle-reinforced 6061 aluminum matrix composites, including promoting precipitate formation, refining precipitate size, and improving distribution uniformity. Compared to other reinforcing particles added to the aluminum matrix, quasicrystalline particles offer significant advantages such as high interfacial bonding strength, strong resistance to high-temperature creep, and excellent corrosion resistance. Specifically:

[0078] The addition of quasicrystalline particles can induce a grain refinement effect in composite materials. As grain boundary pinning agents, quasicrystalline particles hinder grain growth during aging treatment, thereby controlling and refining grain size. Fine grains contribute to improved material strength, fatigue resistance, and plastic deformation capacity. Simultaneously, as grain boundary pinning agents, quasicrystalline particles can inhibit grain growth and grain boundary slip, effectively suppressing creep deformation at high temperatures.

[0079] Furthermore, the addition of quasicrystalline particles helps improve the uniformity of precipitate distribution in the composite material. Quasicrystalline particles can serve as excellent precipitate nuclei, guiding the uniform distribution of the precipitates and reducing excessive accumulation of precipitates in localized areas. Simultaneously, as heterogeneous nucleating agents, quasicrystalline particles can provide excellent precipitate sources, promoting the formation of more precipitates in the composite material during aging treatment. These precipitates can further enhance the strength and hardness of the material, improving its mechanical properties.

[0080] In summary, the addition of quasicrystalline particles after aging treatment of quasicrystalline particle-reinforced 6061 aluminum matrix composites can significantly improve the microstructure and properties of the composites through reinforcement, refinement, and promoting of mutual reactions. This results in enhanced interfacial bonding strength, mechanical properties, corrosion resistance, and thermal stability. These advantages make quasicrystalline particles an important choice for reinforcing phases, significantly improving the performance and application range of aluminum matrix composites.

[0081] The present invention also provides an aluminum-based composite material prepared by the preparation method described in the above technical solution.

[0082] The aluminum-based composite material provided by this invention has excellent interfacial bonding strength, mechanical properties, corrosion resistance and thermal stability.

[0083] The technical solutions of this invention will be clearly and completely described below with reference to the embodiments thereof. Obviously, the described embodiments are only a part of the embodiments of this invention, and not all of them. All other embodiments obtained by those skilled in the art based on the embodiments of this invention without creative effort are within the scope of protection of this invention.

[0084] Example 1

[0085] A method for preparing an aluminum-based composite material comprises the following steps:

[0086] (1) A vacuum arc melting furnace of model QK20-006 was used to prepare (Al) 63 Cu 25 Fe 12 ) 99 Ce1 quasicrystalline master alloy: First, each raw material is ultrasonically cleaned and dried, then processed according to (Al) 63 Cu 25 Fe 12 ) 99 80g of Ce1 was prepared and placed in a copper crucible under vacuum (5×10⁻⁶). -4 Pa, while argon protection is applied, and then the raw materials are melted by electric arc and stirred using an electromagnetic stirring system. The melting current is 50A, and the stirring current and voltage are 30A and 5V, respectively. The mixture is then rapidly cooled using circulating cooling water around the copper crucible wall. The process is then repeated four times by turning and remelting to obtain (Al). 63 Cu 25 Fe 12 ) 99 Ce1 quasicrystalline intermediate alloy;

[0087] (2) The (Al) obtained in step (1) 63Cu 25 Fe 12 ) 99 Ce1 quasicrystalline master alloy was heat-treated at 750℃ for 6 hours, air-cooled, crushed into small pieces, and then manually ground and sieved. Following ball milling, particles with a diameter of 60 μm were obtained as the reinforcing phase. These particles were mixed with 6061 aluminum alloy powder, and the mixture was then placed in a mold and hot-pressed at 490℃ to obtain the composite material. (Al...) 63 Cu 25 Fe 12 ) 99 The Ce1 quasicrystalline master alloy constitutes 20% of the volume of the 6061 aluminum alloy powder; the holding time for hot pressing sintering is 30 min, and the pressure for hot pressing sintering is 30 MPa; the chemical composition of the 6061 aluminum alloy powder is Fe 0.157 wt%, Si 0.56 wt%, Mg 0.81 wt%, Cu 0.166 wt%, Mn 0.071 wt%, Cr 0.051 wt%, Zn 0.031 wt%, Ti 0.002 wt%, and the balance Al;

[0088] (3) The composite material obtained in step (2) is heated to 530°C and kept at that temperature for 1 hour for solution treatment, then water-cooled, and then aged at 170°C for 2 hours. After air cooling, aluminum-based composite material is obtained.

[0089] Comparative Example 1

[0090] Based on Example 1, (Al) 63 Cu 25 Fe 12 ) 99 The grain size of the Ce1 quasicrystalline master alloy was replaced with 120 μm, while other conditions remained unchanged.

[0091] The microstructure of the composite material obtained in step (2) of Example 1 is as follows: Figure 1 and 2 As shown; the microstructure of the composite material obtained in step (2) of Comparative Example 1 is as follows. Figure 3 and 4 As shown.

[0092] from Figures 1-4 It can be seen that the reinforcing phase with a particle size of 60μm has a stronger bond with the matrix. The 60μm reinforcing phase is less prone to defects such as porosity and has a lower probability of diffusion with the matrix.

[0093] Example 2

[0094] Based on Example 1, the heat preservation time for aging treatment was modified to 4 hours, while other conditions remained unchanged.

[0095] Example 3

[0096] Based on Example 1, the heat preservation time for aging treatment was modified to 6 hours, while other conditions remained unchanged.

[0097] Example 4

[0098] Based on Example 1, the heat preservation time for aging treatment was modified to 8 hours, while other conditions remained unchanged.

[0099] Example 5

[0100] Based on Example 1, the heat preservation time for aging treatment was modified to 10 hours, while other conditions remained unchanged.

[0101] Example 6

[0102] Based on Example 1, the heat preservation time for aging treatment was modified to 12 hours, while other conditions remained unchanged.

[0103] Example 7

[0104] Based on Example 1, the heat preservation time for aging treatment was modified to 16 hours, while other conditions remained unchanged.

[0105] Example 8

[0106] Based on Example 1, the heat preservation time for aging treatment was modified to 20 hours, while other conditions remained unchanged.

[0107] Example 9

[0108] Based on Example 1, the heat preservation time for aging treatment was modified to 24 hours, while other conditions remained unchanged.

[0109] Comparative Example 2

[0110] The aging process is omitted from Example 1, while other conditions remain unchanged.

[0111] The microstructure of the aluminum-based composite material prepared in Example 1 is shown in the figure below. Figure 5 As shown; the microstructure of the aluminum-based composite material prepared in Example 2 is shown in the figure. Figure 6 As shown; the microstructure of the aluminum-based composite material prepared in Example 3 is shown in the figure. Figure 7 As shown; the microstructure of the aluminum-based composite material prepared in Example 4 is shown in the figure. Figure 8 As shown; the microstructure of the aluminum-based composite material prepared in Example 5 is shown in the figure. Figure 9 As shown; the microstructure of the aluminum-based composite material prepared in Example 6 is shown in the figure. Figure 10 As shown.

[0112] from Figures 5-10It can be seen that the large white particles are the reinforcing phase retained after aging, and the small white particles are distributed along the grain boundaries, which are identified as the precipitated phase after aging. With the increase of aging time, the number of small particles precipitated along the matrix grain boundaries increases, especially after aging for 10 hours, the number of these small particles increases significantly. However, the common feature of the composite material after aging is that the reinforcing phase of the large white particles has undergone significant diffusion. The reason is that the optimal hot pressing process is 490℃. When the temperature exceeds this, the reinforcing phase will diffuse with the matrix, causing the interior of the reinforcing phase to gradually decompose.

[0113] The Vickers hardness of the aluminum-based composite materials prepared in Examples 1-9 and Comparative Example 2 is as follows: Figure 11 As shown; the tensile strength of the aluminum-based composite materials prepared in Examples 1-9 and Comparative Example 2 is as follows: Figure 12 As shown.

[0114] from Figure 11 and 12 It can be seen that the Vickers hardness and tensile strength of the aluminum matrix composite material first increase and then decrease with increasing aging time, reaching their maximum values ​​when the aging time increases to 10 hours. As the aging time continues to increase, the Vickers hardness first decreases and then remains essentially unchanged. This is because in the early stages of aging, the number of GP zones and β″ phases in the alloy gradually increases, with β″ phase being the most prevalent precipitated phase. As aging time continues, the β″ phase in the alloy becomes highly dispersed, corresponding to a maximum elastic stress, which provides the strongest resistance to dislocation movement. Furthermore, during solution treatment, the composite material cools rapidly with a wide temperature range, resulting in a significant difference in the coefficients of thermal expansion between the reinforcing phase and the matrix. This leads to substantial thermal mismatches and an increase in dislocation density in the matrix. These high-density dislocations interact with the aging-precipitated second phase, enhancing the matrix's resistance to deformation and further improving the Vickers hardness and tensile strength of the composite material. In the later stages of aging, the β′ phase and other metastable phases form in the alloy. These phases gradually grow and coarsen, reducing their resistance to dislocation movement and consequently decreasing the Vickers hardness and tensile strength of the composite material.

[0115] Based on the above experimental results, it can be seen that the hardness and tensile strength of the aluminum-based composite material reached their peak values ​​when the aging time was 10 hours. Therefore, 10 hours was determined to be the optimal aging time. This indicates that the composite material achieved its best performance at this aging time.

[0116] The aluminum-based composite material prepared in Example 5 was observed by TEM to determine... Figure 9 The phase composition consists of small white particles precipitated along the grain boundaries and dispersed in the middle.

[0117] Figure 13 This is a bright-field image of the β phase in the aluminum-based composite material prepared in Example 5; Figure 14 Energy dispersive spectroscopy (EDS) analysis of the β phase in the aluminum-based composite material prepared in Example 5; Figure 15 The image shows the micro-area diffraction pattern of the β phase in the aluminum-based composite material prepared in Example 5.

[0118] from Figures 13-15 It can be seen that after aging treatment at 170℃ for 10 hours, many regular particles were produced. Energy dispersive spectroscopy (EDS) analysis showed that these particles mainly contain aluminum, iron, and some silicon. Selected area electron diffraction (SED) pattern identification confirmed that they are β phase (i.e., Al). 0.5 Fe 0.5 According to relevant literature, the β phase usually contains only aluminum and iron. However, after hot pressing and sintering with the matrix, a small amount of silicon in the matrix diffuses into the reinforcing phase, forming a silicon-containing β phase. This phase still exists after aging and is fine, dispersed, and uniformly distributed, which plays a good role in strengthening the composite material. At the same time, after holding at a temperature for 10 hours, the constituent phases in the alloy include the β phase, the Al2CuMg phase belonging to the orthorhombic crystal system, as well as the β″ phase and a small amount of β′ precipitate phase. The constituent phases are fine and uniformly distributed, which plays a good role in improving the tensile strength and hardness of the composite material.

[0119] Considering the certain phase relationship between the aged precipitates and the aluminum matrix, the material was analyzed using TEM

[001] . Al Observe the direction, among which... Figure 16 Bright-field images of the β′ and β″ phases in the aluminum-based composite material prepared in Example 5; Figure 17 and 18 All Figure 16 High-resolution topography and Fourier transform of bright-field image in the middle region 1; Figure 19 for Figure 16 High-resolution topography and Fourier transform of brightfield image in the middle region 2.

[0120] from Figure 16 The precipitated phase can be seen to be fine and diffusely distributed.

[0121] from Figure 17 and 18 The high-resolution morphology (yellow dashed box) shows that the atoms of the precipitated phase are arranged regularly. Fourier transform and diffraction spot calibration confirm that this region is the β″ phase, with a chemical composition of Mg5Si6 (a = 1.516 nm, b = 0.405 nm, c = 0.674 nm), belonging to the monoclinic crystal system, with a monoclinic angle close to 105.3°. Among all the precipitated phases, the β″ phase has a high coherent strain energy with the matrix and is the most effective reinforcing phase, significantly improving the strength and hardness of the composite material.

[0122] from Figure 19As can be seen from the high-resolution morphology, this region consists of slender needle-like precipitates. FFT analysis reveals that this region is the β′ phase with the chemical formula Mg. 1.8 Si has a hexagonal crystal structure (a = 0.715 nm, c = 1.215 nm). Therefore, after aging at 170℃ for 10 h, the aging precipitation order of the aluminum-based composite material is: β″ phase (Mg5Si6) → β′ phase (Mg 1.8 Si).

[0123] Figure 20 This is a bright-field image of the Al2CuMg phase in the aluminum-based composite material prepared in Example 5; Figure 21 Selected area electron diffraction pattern of the Al2CuMg phase in the aluminum-based composite material prepared in Example 5; Figure 22 The elemental distribution diagram of the aluminum-based composite material prepared in Example 5 is shown below. Figure 23 The image shows the Al element distribution in the aluminum-based composite material prepared in Example 5. Figure 24 The image shows the Cu element distribution in the aluminum-based composite material prepared in Example 5. Figure 25 The image shows the Fe element distribution in the aluminum-based composite material prepared in Example 5. Figure 26 The image shows the Ce element distribution in the aluminum-based composite material prepared in Example 5. Figure 27 The image shows the Mg element distribution in the aluminum-based composite material prepared in Example 5. Figure 28 The image shows the Si element distribution in the aluminum-based composite material prepared in Example 5.

[0124] After aging treatment, aluminum-based composite materials exhibit uniformly distributed white particles in some areas, such as... Figure 20 As shown. To determine the phase composition of these particles, selected area electron diffraction pattern analysis was performed, and the results are as follows. Figure 21 As shown. Based on the diffraction pattern analysis, it was determined to be the Al2CuMg phase, belonging to the orthorhombic crystal system. EDS surface scanning analysis was performed on this region, and the results are as follows. Figures 22-28 As shown.

[0125] from Figures 22-28 As can be seen, the white precipitate is composed of copper, aluminum and magnesium, which is consistent with the selected area electron diffraction pattern analysis results; and magnesium and copper are enriched at the interface, but iron and silicon are not enriched.

[0126] Based on the above analysis, it can be seen that after aging treatment at 170℃ for different holding times, the aluminum-based composite material consists of a β phase and finely dispersed Al2CuMg, β″, and β′ phases. The aging precipitation order of the precipitated phases is: β″ phase (Mg5Si6) → β′ phase (Mg 1.8The β″ phase of Si has a high coherent strain energy with the matrix, which can significantly improve the strength and hardness of the composite material.

[0127] Using the above method, a quasicrystalline reinforced 6061 aluminum-based composite material was successfully prepared using Al-Cu-Fe-Ce quasicrystalline intermediate alloy as the reinforcing phase. This achieved the bonding between the reinforcing phase and the matrix, significantly improved the distribution of the reinforcing phase, and also improved the microstructure after aging, thereby enhancing the mechanical properties and oxidation resistance of the composite material.

[0128] The preparation method provided by this invention has advantages such as feasibility, simple operation, and low preparation cost, which improves the performance of composite materials and has broad application prospects. Quasicrystalline reinforced 6061 aluminum matrix composites were prepared by powder hot pressing sintering. A clear transition layer exists at the interface of the composite material, indicating good wettability between the matrix and the reinforcing phase. The loose structure inside the reinforcing particles promotes the improvement of the wettability of the composite material. Tensile test results show that when the sintering temperature is constant, the tensile strength and elongation at break first increase and then decrease with the increase of the holding time. The sample sintered at 490℃ for 30 min has the highest tensile strength (287.98 MPa) and elongation at break (11.03%). The microstructure of the tensile fracture surface shows that the fracture occurs at both the interface front and inside the particles, indicating that the composite material has good interfacial bonding. Furthermore, although the reaction between quasicrystalline particles and the matrix at the interface can promote the bonding between the matrix metal and the reinforcing particles, the reaction products gradually increase with the increase of the reinforcing phase content, especially the increase of brittle intermetallic compounds, which will have an adverse effect on the performance of the composite material; 1Ce-IQC sintered at 470℃~510℃ p The coefficient of thermal expansion of the 6061 composite material increases with the extension of the holding time. The optimal heat treatment process for the composite material is solution treatment at 530℃ and aging at 170℃ for 10 hours. At this time, the phase composition of the alloy includes fine and uniformly distributed β phase, a small amount of dispersed finely distributed Al2CuMg phase belonging to the orthorhombic crystal system, as well as β″ phase and a small amount of β′ precipitate phase. The fine and uniform distribution of the phase composition plays a good role in improving the strength and hardness of the composite material.

[0129] The above description is only a preferred embodiment of the present invention. It should be noted that for those skilled in the art, several improvements and modifications can be made without departing from the principle of the present invention, and these improvements and modifications should also be considered within the scope of protection of the present invention.

Claims

1. A method for preparing an aluminum-based composite material, comprising the following steps: (1) The Al-Cu-Fe-Ce quasicrystalline intermediate alloy is mixed with the matrix material powder and hot-pressed to obtain the composite material; (2) The composite material obtained in step (1) is subjected to solution treatment and aging treatment in sequence to obtain an aluminum-based composite material; In step (1), the Al-Cu-Fe-Ce quasicrystalline intermediate alloy is (Al 63 Cu 25 Fe 12 ) 99 Ce1 quasicrystalline intermediate alloy; the (Al) 63 Cu 25 Fe 12 ) 99 The preparation method of Ce1 quasicrystalline master alloy is to melt the alloy raw materials sequentially, cool them rapidly, and remelt them by flipping. The particle size of the Al-Cu-Fe-Ce quasicrystalline intermediate alloy in step (1) is 60 μm.

2. The preparation method according to claim 1, characterized in that, In step (1), the Al-Cu-Fe-Ce quasicrystalline intermediate alloy is 5-25% of the volume of the matrix material powder.

3. The preparation method according to claim 1, characterized in that, In step (1), the hot pressing sintering temperature is 460~510℃, the hot pressing sintering time is 20~60min, and the hot pressing sintering pressure is 30MPa.

4. The preparation method according to claim 3, characterized in that, The hot pressing sintering temperature is 490~500℃, and the hot pressing sintering time is 30~50min.

5. The preparation method according to claim 1, characterized in that, The solution treatment temperature in step (2) is 510~550℃, and the solution treatment holding time is 1h.

6. The preparation method according to claim 5, characterized in that, The solution treatment temperature is 520~530℃.

7. The preparation method according to claim 1, characterized in that, The aging treatment temperature in step (2) is 170~190℃, and the aging treatment holding time is 2~24h.

8. The aluminum-based composite material prepared by the preparation method according to any one of claims 1 to 7.

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