AU2020101927A4 - The Method for improving elastic modulus of particle reinforced aluminum-based composite material - Google Patents
The Method for improving elastic modulus of particle reinforced aluminum-based composite material Download PDFInfo
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- C22C32/001—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with only oxides
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- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
- C22C32/0057—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on B4C
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- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0052—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides
- C22C32/0063—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only carbides based on SiC
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- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0068—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only nitrides
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
Abstract
The invention relates to a method for improving the elastic modulus of a particle-reinforced
aluminum-based composite material. The preparation steps are mainly described as follows:
Step 1. Add irregular ceramic particles and industrial pure water into the circulating stirring
ball mill with the mass ratio of 1:5; Step 2, add the ceramic particle slurry to a pressure spray
dryer to atomize into micro-droplets; Step 3, use ultrasonic and mechanical stirring to assist in
cleaning the porous ceramic particle powder, and dry the porous ceramic particle powder. Then
put the porous ceramic particle powder and aluminum alloy block into the mold; Step 4, put
the mold into the protective atmosphere heating furnace, the porous ceramic particle-reinforced
aluminum-based composite material is prepared by the pressureless infiltration method under
a protective atmosphere. The superior effect of the method is that it can obtain a porous particle
reinforced aluminum-based composite material with a lower volume fraction. Compared with
the dense particle-reinforced aluminum-based composite material with the same volume
fraction, the elastic modulus value of the porous particle-reinforced aluminum-based
composite material can be significantly improved.
1 /3
FI,
FIG, 1
Description
1 /3
FIG, 1
The Method for improving elastic modulus of particle reinforced aluminum-based composite material
[01] The invention belongs to the field of metal matrix composite materials, and specifically relates to a method of preparing a kind of improved elastic modulus of particle reinforced aluminum matrix composite materials.
[02] Ceramic particle reinforced aluminum matrix composites have low density, high specific strength, high specific stiffness, high reliability, high thermal conductivity and good friction and wear resistance, it has a broad range of application fields in aerospace, precision instruments, electronic packaging, transportation and other fields. Ceramic particle reinforced aluminum matrix composite material is obtained by physical and chemical composite of aluminum alloy matrix and ceramic particles through external or autogenous methods.
[03] There are many specific preparation methods for ceramic particle reinforced aluminum matrix composites, and the main categories are: stirred casting method, powder metallurgy method and pressureless infiltration method. The stirring casting method has simple process and low production cost, and is suitable for large scale production. However, due to the poor wettability between the ceramic particles and the liquid aluminum alloy, it is difficult for fine-particle ceramics to be stirred and added and dispersed, and gas is easily inhaled during stirring to form air pores and inclusions. The powder metallurgy hot pressing method can prepare aluminum-based composites with medium, low, and high volume fraction reinforcement phases, and the powder mixing process can make the reinforcement phase uniformly distributed in the metal matrix. However, this process equipment is complicated and difficult to scale production. The pressureless infiltration method does not require expensive equipment to prepare ceramic particle-reinforced metal matrix composites. It has the advantages of simple process, lower cost than solid-phase method and traditional liquid-phase method, and easy realization of mass production.
[04] Elastic modulus is one of the important parameters that must be considered when aluminum matrix composites are used as structural materials. The higher the elastic modulus, the greater the stiffness of the material and the greater the property to resist elastic deformation. Generally speaking, the quantitative relationship between the elastic modulus of particle-reinforced aluminum matrix composites and the content of the reinforcement particles has mature theoretical prediction methods without considering the material defects caused by process factors. To increase the elastic modulus of ceramic particle-reinforced aluminum matrix composites, the volume fraction of the reinforcing phase can only be increased. However, the increase of the fraction of the ceramic phase will not only increase the processing difficulty and processing cost of the material to obtaining complex precision parts, but also significantly increase the brittleness of the material and reduce the conductivity of the material, thus affecting the promotion and application of materials.
[05] How to prepare porous ceramic particle reinforced aluminum matrix composites with higher elastic modulus, good electrical conductivity, and easy processing without increasing the particle volume fraction, which has always been a technical problem to be solved in the prior art.
[06] In the prior art, for example, invention patent application number 201510891415.7 discloses an aluminum-based composite material reinforced by mixing high volume fraction B4C and Si particles and a preparation process thereof. The aluminum-based composite material is composed of an Al-Cu-Mg-Co alloy matrix and a mixed reinforcement phase of B4C and Si. By calculating the percentage of volume, the content of the Al-Cu-Mg-Co alloy matrix is 30-45% , the content of B4C is 55-60% , the content of Si is a, 0<a10%. The aluminum-based composite material is prepared by powder metallurgy, which mainly includes the pretreatment ofB4C and Si particles, ball milling and mixing of reinforcement phase with Al alloy matrix powder, powder cold isostatic pressing, vacuum degassing, hot isostatic pressing and other steps. The aluminum-based composite material of the present invention has a density of 2.55-2.60g/cm 3, a bending strength of 450-530MPa, an elastic modulus of 180-220 GPa, a thermal expansion coefficient of 7.6-9.5x10-6K-1, and a thermal conductivity of 70~100W/m-K.
[07] For another example, invention patent application number 201611108212.7 discloses a method for preparing an endogenous dual-phase particle reinforced aluminum matrix composite material, which is characterized in the following steps: (1) According to the molar ratio of TiO2powder and KBF4 powder of 1:2, TiO2powder and KBF4 powder with a particle size of 100-500 mesh are uniformly mixed and dried to obtain mixed powder. The mixed powder is pressed into a blank; (2) The aluminum alloy is heated to 850-950°C to melt and kept for 10-60 minutes, and the mixed powder blank obtained in Step 1 is added to the aluminum alloy melt for endogenous reaction. Stir continuously until the endogenous reaction is completed. After removing the scum, a composite melt containing TiB2 and A203dual-phase ceramic particles is obtained; among the raw materials used.The amount of mixed powder added is 4.91%-50% of the aluminum alloy mass; (3) The temperature of the composite melt obtained in Step 2 is controlled at 720~750°C, andC 2C16 wrapped in aluminum foil is added to the composite melt. And press it to the bottom of the composite melt, then stir for degassing and refining, a refined composite melt is obtained; the addition amount of CC 2 6
wrapped in aluminum foil is 0.2-0.7wt.% of the total mass of the composite melt; (4) The refined composite melt obtained in Step 3 is allowed to stand at 720-750°C 10 min, amd cast into a 200-300°C preheated mold to obtain (TiB2+Al203) dual-phase particle reinforced aluminum matrix composite material.
[08] For another example, the invention patent application number 201710280471.6, the name of invention is a method for preparing a titanium-based metallic glass particle reinforced aluminum-based composite material. It is characterized in the following steps: (1) Powder mixing: Put 5%-20% of titanium-based metallic glass particles and 80%-95% of aluminum alloy powder into a grinding pot, mill on a ball mill for 1-50h to obtain the mixture; (2) Put the mixture of Step 1 into a cold pressing mold at room temperature for cold pressing, and the pressure is 5-20MPa, and obtain the titanium-based metallic glass particle-reinforced aluminum-based composite material blank; (3) Put the titanium-based metallic glass particle-reinforced aluminum-based composite material blank obtained in Step 2 into the aluminum sheath, and then put it into the hot extrusion equipment.Preheat the billet to 350-450°C, preheat the mold to 300-450°C, and then heat-extrude under the conditions of extrusion pressure of 75-15OMPa, extrusion time of 30s-5min, and extrusion ratio of 8-15, and obtain a titanium-based metallic glass particle reinforced aluminum based composite material; the titanium-based metallic glass particles are Ti-Ni-Cu amorphous alloys, and the particle size is less than or equal to 50tm.
[09] The main drawback of the above-mentioned invention patent application is that it is impossible without increasing the volume of particles during the preparation process to obtain a porous ceramic particle-reinforced matrix composite material that meets the requirements of elastic mold and good conductivity, and that is also convenient to prepare.
[010] In order to overcome the defects and deficiencies in the prior art, the present invention provides a method for increasing the elastic modulus of particle-reinforced aluminum-based composite materials, the method includes the following steps:
[011] Step 1. Add irregular ceramic particles with a particle size of 1-10um and industrial pure water according to a mass ratio of 1:5 into the circulating stirring ball mill and mix them evenly. Obtaining a mixture of ceramic particles and industrial pure water; using 1% mass percentage of 7.0% polyacrylic alcohol aqueous solution as the binder and the mixture to be uniformly stirred and dispersed to obtain ceramic particle slurry;
[012] Step 2. Add the ceramic particle slurry to a pressure spray dryer to atomize into micro droplets, which act on the surface tension
[013] Spherical agglomerated particles are formed below, wherein the binder volatilizes to obtain dried spherical porous ceramic particles; the dried spherical porous ceramic particles are fired in a roasting furnace at a roasting temperature of 380°C and a roasting time of 1h. Remove the residual moisture and binder inside the spherical porous ceramic particles, use a sieving machine to sieve the porous ceramic particles to obtain porous ceramic particles with a particle size of 30-500m;
[014] Step 3. Use acetone as the cleaning medium, use ultrasonic and mechanical stirring to assist in cleaning the porous ceramic particle powder. The cleaned porous ceramic particle powder is dried in a dryer at a drying temperature of 150°C. The drying time is lh; according to the required composite material volume, calculate and weigh the porous ceramic particle powder of the corresponding quality into the mold; use the cleaning agent for cleaning the aluminum alloy block to clean the aluminum alloy surface oxide; according to the quantity that matches the porous ceramic particle powder put into the mold, place the cleaned aluminum alloy block on the ceramic particle accumulation in the mold;
[015] Step 4. Put the mold in a protective atmosphere heating furnace, and prepare porous ceramic particle-reinforced aluminum-based composite materials by a pressureless infiltration method in a protective atmosphere;
[016] Step 5 Take out the composite material blank in the mold, remove the remaining aluminum alloy on the surface layer to obtain a porous ceramic particle reinforced aluminum-based composite material, and the obtained composite material is processed by WEDM.
[017] Furthermore, the ceramic particle material in step 1 is any one of alumina A1203, aluminum nitride AlN, silicon carbide SiC, boron carbide B4C and titanium diboride TiB2.
[018] Further, the steps of ultrasonic cleaning of porous ceramic particles in Step 3 are as follows:
[019] Step 3.1, put the porous ceramic particle powder into a washing tank equipped with an ultrasonic cleaner and a mechanical stirrer;
[020] Step 3.2, use acetone as the cleaning medium, and put the cleaning medium into the washing tank at room temperature;
[021] Step 3.3, start the ultrasonic cleaner and mechanical stirrer to clean the porous ceramic particle powder, the ultrasonic cleaning time is not less than 20min;
[022] Step 3.4: Dehydrate and dry the cleaned porous ceramic particles at a temperature of 150°C.
[023] Further, the mold material in step 3 is high-strength graphite. Further, the cleaning agent for cleaning aluminum alloy blocks in Step 3 is prepared by mixing 35 parts by mass of ionized water, 11 parts by mass of trisodium phosphate, 9 parts by mass of sodium hydroxide, 7 parts by mass of veratramine base, 8 parts by mass of sodium dodecyl benzene sulfonate, 13 parts by mass of alcohol ether surfactant, 6 parts by mass of oleamide, 8 parts by mass of sodium molybdate and 4 parts by mass of magnesium hydroxide. Further, the addition amount of the dried porous ceramic particle powder and the addition amount of the aluminum alloy block in step 3 satisfy the following calculation formula (1):
[024] mi=km2 (1),
[025] In formula (1), mi andm2 are the mass of aluminum alloy and porous particles, respectively, and the variable coefficient k is determined according to the selected ceramic particles, and k = 1.0-2.0. Further, the aluminum alloy block in Step 3 comprises a deformed aluminum alloy block or a cast aluminum alloy block.
[026] Further, the protective atmosphere in Step4 is high-purity nitrogen or high purity argon.
[027] Further, the pressureless infiltration method in Step 4 includes the following steps:
[028] Step 4.1, input high-purity nitrogen or high-purity argon into that atmosphere heating furnace, wherein the flow rate of the high-purity nitrogen or high purity argon is 5L/min, and the time for input the high-purity nitrogen or high-purity argon before heating is not less than 30min to drive away oxygen in the atmosphere heating furnace;
[029] Step 4.2, according to the heating rate of 20°C/min, raising the temperature in the atmosphere heating furnace to the temperature required by the pressureless infiltration process, wherein the temperature range is 900-1200°C;
[030] Step 4.3, after the atmosphere heating furnace reaches the set temperature of pressureless infiltration, keeping the temperature for 3h according to the set temperature of the atmosphere heating furnace;
[031] Step 4.4, after the heat preservation time of the atmosphere heating furnace is over, take out the graphite mold at high temperature and cool it in the air to obtain more Pore particle reinforced aluminum matrix composite blank.
[032] The method of the invention has the following beneficial effects:
1. The porous ceramic particle reinforced aluminum matrix composite material with higher elastic modulus and easy processing can be prepared by using the ceramic particles with loose and porous micro-structure as the reinforcing phase without increasing the volume fraction of particles.
2. By using the method of the invention, loose and porous ceramic particles can be obtained by spray drying ceramic particle slurry, atomizing into micro droplets, forming spherical agglomerated particles under the action of surface tension, and then baking.
3. In the method, porous ceramic particles are selected to form a natural accumulation body; The aluminum alloy with the required mass is placed on the stacking body, and the porous ceramic particle reinforced aluminum matrix composite is obtained by spontaneous infiltration of molten aluminum by pressureless infiltration method. The porous ceramic particles in the porous ceramic particle reinforced aluminum matrix composite are evenly distributed, and the aluminum matrix not only penetrates into the gaps between ceramic particles but also into the holes inside the particles. The interface between the particles and the aluminum alloy matrix is well bonded. Compared with common dense ceramic particles, the elastic modulus of the composite corresponding to porous ceramic particles is higher under the same volume fraction.
4. Compared with the traditional method for improving the elastic modulus of aluminum-based composite materials by increasing the content of ceramic particle reinforcing phase, the method of the present invention can obtain aluminum-based composite materials with high elastic modulus without increasing the volume fraction of reinforcing particles.
5. By adopting the method of the invention, the aluminum matrix penetrates into the internal holes of the ceramic particles, which can ensure the good conductivity of the composite material, and the obtained composite material is suitable for processing by adopting cheap WEDM, thus significantly reducing the processing cost.
[033] FIG. 1 is a schematic diagram of the morphology of porous alumina particles with an average particle size of 70tm selected in embodiment 1 of the present invention;
[034] FIG. 2 is a schematic diagram of the microstructure and morphology of the porous alumina reinforced aluminum matrix composite prepared in embodiment 1 of the present invention;
[035] FIG. 3 is a schematic diagram of fracture morphology of the corresponding area of aluminum oxide particles of the aluminum matrix composite material prepared in Embodiment 1 of the present invention.
[036] The present invention will be further explained in detail by examples with reference to the attached drawings. The following examples are for the present invention and the present invention is not limited to the following examples.
[037] Example 1
[038] Step 1, irregular alumina (A1203)particles with a particle size of 1-10tm are selected, and the alumina particles and industrial pure water are added into a circular stirring ball mill according to a mass ratio of 1: 5 to be uniformly stirred and mixed to obtain a mixture of alumina particles and industrial pure water; Uniformly stirring and dispersing 1% of aqueous solution of polypropylene alcohol with a mass percentage concentration of 7% with the mixture to obtain alumina particle slurry;
[039] Step 2, adding the alumina particle slurry into a pressure type spray drier to atomize into micro droplets, forming spherical agglomerated particles under the action of surface tension of the micro droplets, wherein the binder volatilizes to obtain dry spherical porous alumina particles; Roasting dried spherical porous alumina particles in a roasting furnace at 380°C for 1h, removing residual moisture and binder in the spherical porous alumina particles, and sieving the spherical porous ceramic particles with a sieve to obtain porous alumina particle powder with a particle size of 70m;
[040] Step 3, using acetone as a cleaning medium, using ultrasonic waves and a mechanical stirrer to clean porous alumina particle powder at room temperature, cleaning for 20min each time, removing surface liquid after cleaning and standing, cleaning for 5 times, and drying the cleaned porous alumina powder in a dryer at 150°C for 1h;
[041] Step 4, weighing 120g of porous alumina powder and putting the powder into a high purity graphite mold; Machining 6061 aluminum alloy block according to the size of graphite die, and cleaning oxide on the surface of 6061 aluminum alloy block with cleaning agent; 140g of 6061 aluminum alloy block is put on the alumina powder accumulation body in the high purity graphite mold;
[042] Step 5, placing the high purity graphite mold in an atmosphere heating furnace, opening the valve of a high-pressure nitrogen bottle, and inputting protective atmosphere nitrogen into the atmosphere heating furnace, wherein the flow rate of the input nitrogen is 5L/min, and the time for introducing nitrogen before heating is not less than 30min, so as to achieve the purpose of expelling oxygen in the atmosphere heating furnace;
[043] Step 6, preparing the porous alumina particle reinforced aluminum matrix composite material in an atmosphere heating furnace under the action of protective atmosphere by adopting a pressureless infiltration method: firstly, continuously inputting nitrogen into the atmosphere heating furnace; Then, according to the heating rate of 20°C/min, the temperature in the atmosphere heating furnace was raised to 1000°C, and the holding time was 3h, and the porous alumina particle reinforced aluminum matrix composite blank with the size of 80mmx80mmx2Omm was obtained. The volume fraction of the porous alumina reinforced aluminum matrix composite prepared according to this embodiment is only 30%, the bending strength reaches 317MPa, the elastic modulus is 137GPa, and the elastic modulus is 16% higher than that predicted by the classical prediction model.
[044] The volume fraction of the porous alumina reinforced aluminum matrix composite prepared according to this embodiment is only 30%, the bending strength reaches 317MPa, the elastic modulus is 137GPa, and the elastic modulus is 16% higher than that predicted by the classical prediction model. Figs. 1-3 show the powder morphology of porous alumina particles, the microstructure morphology of porous alumina reinforced aluminum matrix composites and the fracture morphology of the corresponding areas of aluminum matrix composites.
[045] Example 2:
[046] Step 1, irregular aluminum nitride particles with a particle size of1-1 Om are selected, and aluminum nitride (AlN) particles and industrial pure water are added into a circular stirring ball mill according to a mass ratio of 1: 5 to be uniformly stirred and mixed to obtain a mixture of aluminum nitride particles and industrial pure water; Uniformly stirring and dispersing 1%- 7 % polypropylene alcohol aqueous solution as a binder with the mixture to obtain aluminum nitride particle slurry;
[047] Step 2, adding the aluminum nitride particle slurry into a pressure type spray drier to atomize into micro droplets, and making the micro droplets work under surface tension Forming spherical agglomerated particles, wherein the binder volatilizes to obtain dry spherical porous aluminum nitride particles; Roasting dried spherical porous aluminum nitride particles in a roasting furnace at 380°C for 1h, removing residual moisture and binder in the spherical porous aluminum nitride particles, and sieving the spherical porous aluminum nitride particles by using a sieving machine to obtain porous aluminum nitride particle powder with a particle size of 200tm;
[048] Step 3, using acetone as a cleaning medium, using ultrasonic waves and a mechanical stirrer to clean porous alumina particle powder at room temperature, cleaning for 20min each time, removing surface liquid after cleaning and standing, cleaning for 5 times, and drying the cleaned porous aluminum nitride powder in a dryer at 150 °C for lh;
[049] Step 4, weighing 1OOg of dried porous aluminum nitride powder and putting the powder into a mold; According to the size of graphite die, process lxxx aluminum alloy with required quality and size, and clean the oxide on the surface of lxxx aluminum alloy with cleaning agent; 140g lxxx aluminum alloy block is placed on the aluminum nitride powder accumulation body in the high purity graphite mold;
[050] Step 5, placing the high purity graphite mold in an atmosphere heating furnace, opening the valve of a high-pressure nitrogen bottle, and inputting protective atmosphere nitrogen into the atmosphere heating furnace, wherein the flow rate of the input nitrogen is 5L/min, and the time for introducing nitrogen before heating is not less than 30min, so as to achieve the purpose of expelling oxygen in the atmosphere heating furnace;
[051] Step 6, preparing porous alumina particles by pressureless infiltration method in an atmosphere heating furnace under the action of protective atmosphere Strong aluminum matrix composite material: firstly, nitrogen is continuously input into the atmosphere heating furnace; Then, according to the heating rate of 20°C/min, the temperature in the atmosphere heating furnace was raised to 1100°C, and the holding time was 3h, and the porous alumina particle reinforced aluminum matrix composite blank with the size of 80mmx80mmx20mm was obtained.
[052] The volume fraction of porous aluminum nitride reinforced aluminum matrix composite prepared according to this embodiment is only 30%, and its bending strength value reaches 50OMPa, elastic modulus value is 141GPa, and the elastic modulus value is 13% higher than the predicted value of classical prediction model.
[053] Example 3:
[054] Step 1, irregular silicon carbide (SiC) particles with a particle size of 1 m and industrial pure water are selected and added into a circular stirring ball mill according to a mass ratio of 1: 5 to be uniformly stirred and mixed to obtain a mixture of SiC particles and industrial pure water; Uniformly stirring and dispersing 1%- 7
% polypropylene alcohol aqueous solution as a binder with the mixture to obtain silicon carbide particle slurry;
[055] Step 2, adding the silicon carbide particle slurry into a pressure-type spray drier to atomize into micro droplets, wherein the micro droplets form spherical agglomerated particles under the action of surface tension, and the binder volatilizes to obtain dry spherical porous silicon carbide particles; Roasting dried spherical porous silicon carbide particles in a roasting furnace at 380 °C for lh, removing residual
moisture and binder in the spherical porous silicon carbide particles, and sieving the spherical porous silicon carbide particles by using a sieving machine to obtain porous silicon carbide powder with a particle size of 500 m ;
[056] Step 3, using acetone as cleaning medium, using ultrasonic cleaning method to clean porous silicon carbide powder at room temperature for 20min each time, removing surface liquid after cleaning and standing, cleaning for 5 times, stirring the cleaned porous silicon carbide powder with a mechanical stirrer, and then drying the porous silicon carbide powder in a dryer at 150°C for lh;
[057] Step 4, weighing 100g of dried porous silicon carbide powder and putting the powder into a mold; According to the size of high purity graphite die 2xxx aluminum alloy, use cleaning agent to clean the surface oxide; 140g 2xxx aluminum alloy block is placed on the porous silicon carbide powder accumulation body in the high purity graphite mold; Step 5, placing the high purity graphite mold in an atmosphere heating furnace, opening the valve of a high-pressure nitrogen bottle, and inputting protective atmosphere nitrogen into the atmosphere heating furnace, wherein the flow rate of the input nitrogen is 5L/min, and the time for introducing nitrogen before heating is not less than 30min, so as to achieve the purpose of expelling oxygen in the atmosphere heating furnace;
[058] Step 6, preparing the porous silicon carbide particle reinforced aluminum matrix composite material in an atmosphere heating furnace under the action of protective atmosphere by adopting a pressureless infiltration method: firstly, continuously inputting nitrogen into the atmosphere heating furnace; Then, according to the heating rate of 20°C/min, the temperature in the atmosphere heating furnace was raised to 900°C, and the heat preservation time was 3h to obtain the porous alumina particle reinforced aluminum matrix composite blank with the size of mmx8Ommx2Omm;
[059] The volume fraction of porous silicon carbide reinforced aluminum matrix composite prepared according to this example is 40%, the bending strength value is 380MPa, the elastic modulus is 171GPa, and the elastic modulus value is 11% higher than the predicted value of the classical prediction model.
[060] Example 4:
[061] Step 1, irregular boron carbide (B4C) particles with a particle size of 1 m and industrial pure water are selected and added into a circular stirring ball mill according to a mass ratio of 1: 5 to be uniformly stirred and mixed to obtain a mixture of boron carbide particles and industrial pure water; Uniformly stirring and dispersing 1%- 7 % polypropylene alcohol aqueous solution as a binder with the mixture to obtain boron carbide particle slurry;
[062] Step 2, adding the boron carbide particle slurry into a pressure type spray drier to atomize into micro droplets, wherein the micro droplets form spherical agglomerated particles under the action of surface tension, and the binder volatilizes to obtain dry spherical porous boron carbide particles; Roasting dried spherical porous boron carbide particles in a roasting furnace at 380°C for lh, removing residual moisture and binder in the spherical porous boron carbide particles, and sieving the spherical porous boron carbide particles by using a sieving machine to obtain porous boron carbide powder with a particle size of 50[m ;
[063] Step 3, using acetone as cleaning medium, using ultrasonic cleaning method to clean porous boron carbide powder at room temperature, cleaning for 20min each time, removing surface liquid after cleaning and standing, cleaning for 5 times, stirring the cleaned porous boron carbide powder with a mechanical stirrer, and drying the porous boron carbide powder in a dryer at 150 °C for lh;
[064] Step 4, weighing 70g of dried porous boron carbide powder and putting the powder into a mold; Machining 3xxx aluminum alloy according to the size of high purity graphite die, cleaning surface oxide with cleaning agent; 140g 3xxx aluminum alloy block is placed on the porous boron carbide powder accumulation body in the high purity graphite mold; Step 5, placing the high purity graphite mold in an atmosphere heating furnace, opening the valve of a high-pressure nitrogen bottle, and inputting protective atmosphere nitrogen into the atmosphere heating furnace, wherein the flow rate of the input nitrogen is 5L/min, and the time for introducing nitrogen before heating is not less than 30min, so as to achieve the purpose of expelling oxygen in the atmosphere heating furnace;
[065] Step 6, preparing the porous alumina particle reinforced aluminum matrix composite material in an atmosphere heating furnace under the action of protective atmosphere by adopting a pressureless infiltration method: firstly, continuously inputting nitrogen into the atmosphere heating furnace; Then, according to the heating rate of 20°C/min, the temperature in the atmosphere heating furnace was raised to 1200°C, and the heat preservation time was 3h to obtain the porous alumina particle reinforced aluminum matrix composite blank with the size of 80mmx80mmx20mm;
[066] The porous boron carbide particle reinforced aluminum matrix composite prepared according to this example has a volume fraction of 28% and a bending strength The value is 400MPa, the elastic modulus value is 138GPa, and the elastic modulus value is 10% higher than that predicted by the classical prediction model.
[067] Example 5:
[068] Step 1, porous titanium diboride (TiB2) particles with a particle size of 1 tm and industrial pure water are selected and added into a circular stirring ball mill according to a mass ratio of 1: 5 to be uniformly stirred and mixed to obtain a mixture of titanium diboride particles and industrial pure water; Uniformly stirring and dispersing 1%-7% polypropylene alcohol aqueous solution as a binder with the mixture to obtain titanium diboride particle slurry;
[069] Step 2, adding titanium diboride particle slurry into a pressure type spray drier to atomize into micro droplets, wherein the micro droplets form spherical agglomerated particles under the action of surface tension, and the binder volatilizes to obtain dry spherical porous boron carbide particles; Roasting dried spherical porous titanium diboride particles in a roasting furnace at 380°C for 1h, removing residual moisture and binder in the spherical porous titanium diboride particles, and sieving the spherical porous titanium diboride particles by using a sieving machine to obtain porous titanium diboride powder with a particle size of 30[m;
[070] Step 3, using acetone as cleaning medium, cleaning porous titanium diboride powder by ultrasonic cleaning method at room temperature for 20min each time, removing surface liquid after cleaning and standing, cleaning for 5 times, stirring the cleaned porous titanium diboride powder by using a mechanical stirrer, and drying the porous titanium diboride powder in a dryer at 150°C for 1h;
[071] Step 4, weighing 140g of dried porous titanium diboride powder and putting into a mold; Machining 4xxx aluminum alloy block according to the die size of high purity graphite Institute, and cleaning oxides on the surface of 4xxx aluminum alloy block with cleaning agent; 140g 4xxx aluminum alloy block is placed on the porous titanium diboride powder accumulation body in the high purity graphite mold;
[072] Step 5, placing the high purity graphite mold in an atmosphere heating furnace, opening the valve of a high-pressure nitrogen bottle, and inputting protective atmosphere nitrogen into the atmosphere heating furnace, wherein the flow rate of the input nitrogen is 5L/min, and the time for introducing nitrogen before heating is not less than 30min, so as to achieve the purpose of expelling oxygen in the atmosphere heating furnace; Step 6, preparing the porous alumina particle reinforced aluminum matrix composite material in an atmosphere heating furnace under the action of protective atmosphere by adopting a pressureless infiltration method: firstly, continuously inputting nitrogen into the atmosphere heating furnace; Then, according to the heating rate of 20°C/min, the temperature in the atmosphere heating furnace was raised to 900°C, and the heat preservation time was 3h to obtain the porous alumina particle reinforced aluminum matrix composite blank with the size of 80mmx80mmx20mm; The porous titanium diboride particle reinforced aluminum matrix composite prepared according to this example has a volume fraction of 40% and a bending strength The value is 800MPa, the elastic modulus value is 186GPa, and the elastic modulus value is 13% higher than that predicted by the classical prediction model. The porous alumina particle reinforced aluminum matrix composites obtained in the above embodiments 1 to 5 of the present invention can be processed by WEDM, and can be used as a base material in the fields of aerospace, precision instruments, electronic packaging and transportation.
[073] To sum up, it can be clearly seen from the research results of the above five specific examples that porous ceramic particles can be used to obtain porous particle reinforced aluminum matrix composites with lower volume fraction. Compared with dense particle reinforced aluminum matrix composites with the same volume fraction, the elastic modulus of porous particle reinforced aluminum matrix composites can be significantly improved.
[074] The above embodiments are only used to illustrate the technical scheme of the present invention, but not to limit it. Although the present invention has been described in detail with reference to the above embodiments, ordinary people in the field can still modify or replace the specific embodiment of the present invention, and any modification or equivalent replacement that does not deviate from the spirit and scope of the present invention is within the protection scope of the pending claims of the present invention.
[075] Although the invention has been described with reference to specific examples, it will be appreciated by those skilled in the art that the invention may be embodied in many other forms, in keeping with the broad principles and the spirit of the invention described herein.
[076] The present invention and the described embodiments specifically include the best method known to the applicant of performing the invention. The present invention and the described preferred embodiments specifically include at least one feature that is industrially applicable.
Claims (8)
1. A method for improving the elastic modulus of particle reinforced aluminum matrix composites, which comprises the following steps:
Step 1, adding irregular ceramic particles with particle size of 1-10im and industrial pure water into a circular stirring ball mill according to a mass ratio of 1: 5, uniformly stirring and mixing to obtain a mixture of ceramic particles and industrial pure water; Evenly stirring the mixture with 1% of polypropylene alcohol aqueous solution used as a binder with a mass percentage concentration of 7.0% to obtain ceramic particle slurry;
Step 2, adding the ceramic particle slurry into a pressure type spray drier to atomize into micro droplets, and the micro droplets act under surface tension Forming spherical agglomerated particles, wherein the binder volatilizes to obtain dry spherical porous ceramic particles; Baking dried spherical porous ceramic particles in a baking furnace at 380°C for lh, removing residual moisture and binder in the spherical porous ceramic particles, and sieving the porous ceramic particles by using a sieving machine to obtain porous ceramic particle powder with a particle size of 30-500m;
Step 3, acetone is used as a cleaning medium, ultrasonic waves and mechanical stirring are used to assist in cleaning the porous ceramic particle powder, and the cleaned porous ceramic particle powder is placed in a dryer for drying at 150°C for lh; According to the volume of the required composite material, the porous ceramic particle powder with corresponding mass is weighed and put into a mold; Cleaning oxides on the surface of aluminum alloy with a cleaning agent for cleaning aluminum alloy blocks; Placing the aluminum alloy block on the ceramic particle accumulation body in the mold according to the matched quantity of the porous ceramic particle powder in the mold;
Step 4, putting the mold into a protective atmosphere heating furnace, and preparing the porous ceramic particle reinforced aluminum matrix composite material by adopting a pressureless infiltration method in the protective atmosphere;
Step 5, taking out that composite material blank in the die, removing the residual aluminum alloy on the surface lay to obtain the porous ceramic particle reinforced aluminum-based composite material, and machining the obtain composite material by adopting electric spark wire cutting.
2. The method for improving elastic modulus of particle reinforced aluminum matrix composite according to claim 1, wherein the ceramic particle material in step 1 is any one of alumina, aluminum nitride, silicon carbide, boron carbide and titanium diboride.
3. The method for improving elastic modulus of particle reinforced aluminum matrix composite according to claim 1, characterized in that the ultrasonic cleaning of porous ceramic particle powder in step 3 comprises the following steps:
Step 3.1, putting porous ceramic particle powder into a washing tank provided with an ultrasonic cleaner and a mechanical stirrer;
Step 3.2, taking acetone as a cleaning medium, and putting the cleaning medium into a washing tank at room temperature;
Step 3.3, starting an ultrasonic cleaner and a mechanical stirrer to clean the porous ceramic particle powder, wherein the ultrasonic cleaning time is not less than min ; ; Step 3.4, dehydrating and drying the cleaned porous ceramic particle powder at 150°C
4. The method for improving elastic modulus of particle reinforced aluminum matrix composite according to claim 1, characterized in that the number of porous ceramic particle powder and aluminum alloy blocks put into the mold in step 3 is calculated according to the following formula:
m1=km2 (2),
In formula (1), ml and m2 are the mass of aluminum alloy and porous particles, respectively, and the variable coefficient k is determined according to the selected ceramic particles, and k = 1.0 ~ 2.0.
5. The method for improving the elastic modulus of particle reinforced aluminum matrix composites according to claim 1, characterized in that the cleaning agent for cleaning aluminum alloy blocks in step 3 is prepared by mixing 35 parts by mass of ionized water, 11 parts by mass of trisodium phosphate, 9 parts by mass of sodium hydroxide, 7 parts by mass of veratramine base, 8 parts by mass of sodium dodecyl benzene sulfonate, 13 parts by mass of alcohol ether surfactant, 6 parts by mass of oleamide, 8 parts by mass of sodium molybdate and 4 parts by mass of magnesium hydroxide.
6. The method for improving elastic modulus of particle reinforced aluminum matrix composite according to claim 1, characterized in that the die material in step 3 is high-strength graphite.
7. The method for improving elastic modulus of particle reinforced aluminum matrix composite according to claim 1, wherein the aluminum alloy block comprises a deformed aluminum alloy block or a cast aluminum alloy block.
8. The method for improving elastic modulus of particle reinforced aluminum matrix composites according to claim 1, characterized in that the pressureless infiltration method in step 4 comprises the following steps:
Step 4.1, input high-purity nitrogen or high-purity argon into that atmosphere heating furnace, wherein the flow rate of the high-purity nitrogen or high-purity argon is 5L/min, and the time for input the high-purity nitrogen or high-purity argon before heating is not less than 30min to drive away oxygen in the atmosphere heating furnace;
Step 4.2, according to the heating rate of 20°C/min, raising the temperature in the atmosphere heating furnace to the temperature required by the pressureless infiltration process, with the temperature range being 900-1200°C;
Step 4.3, after the atmosphere heating furnace reach the set temperature of pressureless infiltration, keeping the temperature for 3h according to the set temperature of the atmosphere heat furnace; step 4.4, after the heat preservation time of the atmosphere heating furnace is finished, taking out the graphite mold at high temperature and cooling in the air to obtain a porous particle reinforced aluminum matrix composite material blank.
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