CN115896555A - Aluminum-based composite material and preparation method and application thereof - Google Patents
Aluminum-based composite material and preparation method and application thereof Download PDFInfo
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- 239000002131 composite material Substances 0.000 title claims abstract description 77
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 43
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 43
- 238000002360 preparation method Methods 0.000 title claims abstract description 7
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 69
- 239000000956 alloy Substances 0.000 claims abstract description 69
- 239000000843 powder Substances 0.000 claims abstract description 63
- 239000002245 particle Substances 0.000 claims abstract description 30
- 229910003407 AlSi10Mg Inorganic materials 0.000 claims abstract description 24
- 238000004519 manufacturing process Methods 0.000 claims abstract description 18
- 238000007639 printing Methods 0.000 claims description 33
- 239000011159 matrix material Substances 0.000 claims description 28
- 238000000034 method Methods 0.000 claims description 28
- 239000000758 substrate Substances 0.000 claims description 15
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 claims description 12
- 238000000498 ball milling Methods 0.000 claims description 8
- 229910000838 Al alloy Inorganic materials 0.000 claims description 6
- 239000011261 inert gas Substances 0.000 claims description 6
- 229910052751 metal Inorganic materials 0.000 claims description 5
- 239000002184 metal Substances 0.000 claims description 5
- 239000004411 aluminium Substances 0.000 claims description 3
- 238000002156 mixing Methods 0.000 claims description 2
- 229910018125 Al-Si Inorganic materials 0.000 claims 1
- 229910018520 Al—Si Inorganic materials 0.000 claims 1
- 238000010146 3D printing Methods 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 63
- 239000007787 solid Substances 0.000 description 22
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 8
- 239000000654 additive Substances 0.000 description 7
- 230000000996 additive effect Effects 0.000 description 7
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 7
- 238000000227 grinding Methods 0.000 description 7
- 239000001301 oxygen Substances 0.000 description 7
- 229910052760 oxygen Inorganic materials 0.000 description 7
- 238000005516 engineering process Methods 0.000 description 5
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- 241000251468 Actinopterygii Species 0.000 description 4
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 239000000463 material Substances 0.000 description 4
- 238000002844 melting Methods 0.000 description 4
- 230000008018 melting Effects 0.000 description 4
- 238000000879 optical micrograph Methods 0.000 description 4
- 239000002356 single layer Substances 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 230000002787 reinforcement Effects 0.000 description 3
- 238000003892 spreading Methods 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- 238000005054 agglomeration Methods 0.000 description 2
- 230000002776 aggregation Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
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- 238000010521 absorption reaction Methods 0.000 description 1
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- 239000013078 crystal Substances 0.000 description 1
- 238000001887 electron backscatter diffraction Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 238000007648 laser printing Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 229910052755 nonmetal Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
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Abstract
The invention provides an aluminum-based compositeA composite material and a preparation method and application thereof. The aluminum-based composite material contains AlSi10Mg alloy and AlFeCrCoNi 2.1 High entropy alloy. The invention is prepared by adding AlFeCrCoNi 2.1 Preparing the high-entropy alloy particles and the AlSi10Mg alloy powder into composite powder with good fluidity, then performing 3D printing on the composite powder, and performing laser scanning, fusing and forming to prepare the aluminum-based composite material. The aluminum-based composite material has good strength and hardness, and can be applied to manufacturing of light-weight and high-performance complex parts of aviation, aerospace, automobiles and the like.
Description
Technical Field
The invention belongs to the field of materials, and particularly relates to an aluminum-based composite material as well as a preparation method and application thereof.
Background
Laser additive manufacturing technology is becoming an effective approach to solving the problem of aircraft complex component manufacturing, and is particularly represented by Selective Laser Melting (SLM) additive manufacturing technology based on a powder bed. The laser additive manufacturing technology of the aluminum-based composite material can greatly reduce the weight of parts and reduce the cost, so the laser additive manufacturing technology of the aluminum alloy is highly emphasized in the field of manufacturing light-weight and high-performance complex parts such as aviation, aerospace, automobiles and the like.
In recent years, siC and Al have been used 2 O 3 、TiB 2 The additive manufacturing technology of the ceramic particle reinforced aluminum matrix composite material is developed rapidly. However, the introduced particle reinforced phase and the aluminum alloy have great difference in physical and chemical properties, so that the plasticity and toughness of the composite material are poor, and the application of the structural material with good comprehensive mechanical properties is limited.
The High Entropy Alloy (HEA) is a solid solution which is composed of five or more than five equal or nearly equal molar metal (including partial non-metal) elements and takes a certain single phase as a matrix, has the characteristics of High temperature creep resistance, high temperature oxidation resistance, corrosion resistance, high strength, high hardness and the like, and when the High entropy alloy is taken as a reinforcement, the High entropy alloy is derived from the natural interface bonding characteristic between metal and metal, and the interface wettability and the interface compatibility between the High entropy alloy and an aluminum alloy matrix are good, so that the bottleneck of the traditional ceramic reinforced aluminum-based composite material can be effectively broken through, and the aluminum-based composite material with good comprehensive mechanical properties can be prepared. Meanwhile, by combining a Selective Laser Melting (SLM) process, the composite material component with high surface precision and any complex shape can be prepared, and the reinforcement can be uniformly dispersed in the matrix, so that a better reinforcement effect is achieved on the matrix, and the aluminum matrix composite with high strength, high hardness and high wear resistance is prepared.
In view of the above, there is a need to develop an additive manufacturing method for a high-entropy alloy reinforced aluminum-based composite material, so as to solve the above problems.
Disclosure of Invention
The present invention has been made to solve at least one of the above-mentioned problems occurring in the prior art. To this end, the present invention proposes, in a first aspect, an aluminum matrix composite having high hardness and strength.
The second aspect of the invention provides a preparation method of the aluminum matrix composite material.
The third aspect of the invention proposes the application of the aluminum matrix composite material.
According to a first aspect of the present invention, an aluminum-based composite material is proposed, said aluminum-based composite material containing an AlSi10Mg alloy and AlFeCrCoNi 2.1 High entropy alloy.
In some embodiments of the invention, the AlFeCrCoNi is in the aluminum matrix composite 2.1 The content of the high-entropy alloy is 4.5-5 wt.%.
In some embodiments of the invention, the content of the AlSi10Mg alloy in the aluminum-based composite material is 95wt.% to 95.5wt.%.
In the present invention, the AlFeCrCoNi 2.1 The high-entropy alloy is a typical high-temperature-resistant high-entropy alloy, and the melting point of the high-entropy alloy can reach more than 1500 DEG COther high-entropy alloys researched at present can be dissolved in a matrix in the forming process to cause forming defects and influence the mechanical property, and the AlFeCrCoNi 2.1 The high-entropy alloy powder material is already industrialized, and other high-entropy alloys can not be prepared into powder materials meeting the requirements.
According to a second aspect of the present invention, there is provided a method for preparing the aluminum matrix composite material according to the first aspect, comprising the steps of:
s1: alSi10Mg alloy powder and AlFeCrCoNi 2.1 Ball-milling and mixing the high-entropy alloy particles to obtain AlFeCrCoNi 2.1 The method comprises the following steps of (1) paving composite powder/AlSi 10Mg on a substrate of a forming cabin of the SLM metal 3D printer to form a composite powder layer;
s2: under the protection of inert gas, carrying out laser scanning fusing and forming on the composite powder layer;
s3: and repeating the step S1 and the step S2 to realize layer-by-layer laser scanning, printing and forming to obtain the aluminum matrix composite.
In the present invention, the actual printing process further includes: establishing a three-dimensional model of a workpiece, obtaining a plane outline model of each layer by using slicing software, wiping parts such as a substrate, a powder cylinder, a scraper and the like by using alcohol before operation, and filling inert gas into a forming cabin for protection; and scraping the powder from the powder cylinder to the forming cabin by a scraper, scanning the printing path of the laser beam according to the model, driving the forming substrate to descend by one layer thickness height by the forming cabin after scanning is finished by one layer, paving the powder again, scanning and printing the laser again according to the next layer of model, and finally piling to obtain the composite material part.
In some embodiments of the invention, the AlSi10Mg alloy powder in S1 is spheroidal with an average particle size of 13 μm to 53 μm.
In some embodiments of the invention, the AlFeCrCoNi as described in S1 2.1 The high-entropy alloy particles are spheroidal, and the average particle size is 13-53 mu m.
In some embodiments of the invention, the AlFeCrCoNi as described in S1 2.1 The mass of the high-entropy alloy particles accounts for 4.5-5 wt% of the composite powder.
In some embodiments of the invention, the AlSi10Mg alloy powder in S1 comprises the following components in mass percent: si: 9.87-10 wt.%; fe: 0.08-0.09 wt.%; mg: 0.30-0.32 wt.%; zn <0.01wt.%; ti:0.014 to 0.015wt.%; cu: 0.019-0.02 wt.%; ni <0.01wt.%; o: <0.04wt.%, the balance being Al and unavoidable impurities.
In some embodiments of the invention, the AlFeCrCoNi as described in S1 2.1 Element content Al in the high-entropy alloy particles: co: cr: fe:1, ni.
In some embodiments of the invention, the ball-milled and mixed milling balls of S1 have a diameter of 5mm to 15mm.
In some embodiments of the invention, the grinding balls have a mass that is comparable to the mass of the AlSi10Mg alloy powder, alFeCrCoNi 2.1 The mass ratio of the high-entropy alloy particles is 1: (10 to 11).
In some embodiments of the invention, the rotation speed of the ball mill in S1 is 150 r/min-200 r/min, and the time is 2 h-3 h.
In some embodiments of the invention, the pressure in the forming chamber in S1 is 5kPa to 8kPa.
In some embodiments of the invention, the oxygen content in the forming chamber in S1 is < 100ppm.
In some embodiments of the invention, the inert gas in S2 is selected from nitrogen or argon.
In some embodiments of the present invention, the substrate in S1 is an Al — Si-based aluminum alloy plate.
In some embodiments of the invention, the thickness of the composite powder layer in S1 is 30 μm to 35 μm.
In some embodiments of the present invention, the laser power of the laser scan in S2 is 260W to 340W.
In some embodiments of the present invention, the scanning speed of the laser scanning in S2 is 1200mm/S to 1300mm/S.
In some embodiments of the present invention, the layer-by-layer laser scanning printing forming in S3 specifically includes: the laser scanning path of each layer and the laser scanning path of the previous layer form an included angle of 60-67 degrees for printing and forming.
In the invention, in the process of printing and forming each layer, a laser beam firstly forms an internal solid plane according to a preset scanning path, and after the internal solid plane is formed, the laser beam sequentially carries out scanning and forming of an external outline from inside to outside around the edge of the internal solid plane of the layer, and finally the forming of the single-layer printing layer is completed. The laser power and scan speed for printing the internal solid plane is consistent with the laser power and scan speed for printing the external profile.
According to a third aspect of the present invention, there is provided the use of the aluminium matrix composite material of the first aspect in the manufacture of aerospace and automotive parts.
The invention has the beneficial effects that:
the internal solid structure of the aluminum-based composite material shows that eutectic Si is distributed in an alpha-Al matrix in a network form, and AlFeCrCoNi can be observed 2.1 The high-entropy alloy particles are uniformly distributed in the matrix, and AlFeCrCoNi can be observed 2.1 The high-entropy alloy particles form an obvious transition layer between the matrixes, the thickness of the transition layer is 1-2 mu m, and the aluminum matrix composite material has higher hardness and strength.
The aluminum matrix composite material is simple to prepare and suitable for large-scale production.
The aluminum-based composite material can be used for manufacturing light-weight and high-performance complex parts of aviation, aerospace, automobiles and the like due to the characteristics of good comprehensive mechanical property, portability and low cost.
Drawings
The invention is further described with reference to the following figures and examples, in which:
FIG. 1 shows (a) the microstructure of AlSi10Mg alloy powder used in example 1 of the present invention and (b) AlFeCrCoNi alloy powder used in example 1 of the present invention 2.1 The micro-morphology of the high-entropy alloy particles;
FIG. 2 shows an Al-based composite material (AlFeCrCoNi) obtained in example 1 of the present invention 2.1 /A1Si10 Mg) optical micrographs of the internal solid structure in the vertical (a) and horizontal (b) directions;
FIG. 3 shows an aluminum-based composite material (AlFeCrCoNi) prepared according to example 1 of the present invention 2.1 Single AlFeCrCoNi in A1Si10 Mg) 2.1 EDS line scan of the particles;
FIG. 4 shows an aluminum-based composite material (AlFeCrCoNi) prepared according to example 1 of the present invention 2.1 A1Si10 Mg) spectrum;
FIG. 5 is an optical micrograph of the internal solid structure in the vertical (a) and horizontal (b) directions of an AlSi10Mg alloy prepared according to a comparative example of the present invention.
Detailed Description
The concept and technical effects of the present invention will be clearly and completely described below in conjunction with the embodiments to fully understand the objects, features and effects of the present invention. It is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments, and those skilled in the art can obtain other embodiments without inventive effort based on the embodiments of the present invention, and all embodiments are within the protection scope of the present invention.
The AlSi10Mg alloy powder used in the comparative examples below consists of, in mass percent: si:9.87wt.%; fe:0.09wt.%; mg:0.3wt.%; zn: <0.01wt.%; ti:0.014wt.%; cu:0.019wt.%; ni: <0.01wt.%;0:0.04wt.%, the balance being Al and unavoidable impurities.
AlFeCrCoNi used in comparative examples of the following examples 2.1 High entropy alloy particles, in percent of element content, alFeCrCoNi 2.1 The high-entropy alloy particles consist of the following components: al:17.16at.%; co:17.48at.%; cr:16.02at.%; fe:16.00at.%; ni:33.34at.%.
The slicing software used was Materialise Magics.
Example 1
The embodiment prepares the aluminum matrix composite material, and the specific process is as follows:
establishing a three-dimensional model of a workpiece, obtaining a plane profile model of each layer by slicing software, wiping parts such as a substrate, a powder cylinder, a scraper and the like by alcohol before a test, and filling argon into a forming cabin for protection, wherein the pressure in the forming cabin is kept at 5-8 kPa, and the oxygen content is lower than 100ppm.
(1) 95wt.% of AlSi10Mg alloy powder and 5wt.% of AlFeCrCoNi in terms of mass fraction 2.1 Adding high-entropy alloy particles into a ball milling tank, simultaneously filling Ar gas into the ball milling tank for protection, wherein the oxygen content in the tank is lower than 100ppm, simultaneously adding grinding balls into the tank, wherein the mass ratio of the grinding balls to powder is 1 2.1 The AlSi10Mg composite powder is subjected to scraper treatment to obtain AlFeCrCoNi 2.1 The AlSi10Mg composite powder is scraped to a forming cabin from a powder cylinder, and an AlSi10Mg alloy substrate is flatly paved on the forming cabin to form a composite powder layer with the thickness of 30-35 mu m;
(2) And under the protection of Ar gas, performing laser scanning forming on the composite powder layer: in the process of printing and forming each layer, a laser beam forms an internal solid plane according to a scanning path preset according to a model, after the internal solid plane is formed, the laser beam sequentially carries out scanning and forming of an external outline from inside to outside around the edge of the internal solid plane of the layer, and then the single-layer printing process is completed. And executing the forming process of the printing layer by layer, after scanning one layer, driving the forming substrate to descend by one layer thickness height by the forming cabin, then spreading powder again, scanning and printing the laser again according to the next layer of model, and finally piling to obtain the aluminum-based composite material workpiece. Wherein the laser scanning path of each layer forms an included angle of 60-67 degrees with the laser scanning path of the previous layer until the AlFeCrCoNi is finished 2.1 Manufacturing and forming of the/AlSi 10Mg composite material. The laser power and scanning speed for printing the internal solid plane is consistent with printing the external profile. The laser process parameters adopted in the embodiment are as follows: the laser power was 260W, the scanning speed was 1300mm/s, the scanning pitch was 130 μm, and the layer thickness was 30 μm.
FIG. 1 (a) shows the microstructure of the AlSi10Mg alloy powder used in this exampleThe appearance is that as can be seen from the figure (a), the alloy powder is in a sphere-like shape and is occasionally seen as satellite powder, more than 90% of the powder particle size of the alloy powder in the embodiment is concentrated between 13 mu m and 53 mu m, and basically no agglomeration exists, so that the compactness of an aluminum alloy product is favorably improved; FIG. 1 (b) shows AlFeCrCoNi employed in this example 2.1 The microstructure of the high-entropy alloy powder can be seen from (b), the alloy can be substantially spherical, satellite particles exist, more than 80% of the powder particle size of the alloy powder in the embodiment is concentrated between 13 and 53 mu m, and the alloy powder is substantially free of agglomeration.
FIG. 2 shows an aluminum matrix composite (AlFeCrCoNi) prepared according to this example 2.1 Optical micrographs of the internal structure of/AlSi 10 Mg) in the vertical (a) and horizontal (b) directions. Macroscopically, the tissues in the vertical direction are fish scales, and are cellular grains which are distributed according to layers, the diameter of a single fish scale tissue is 70-130 mu m, and the fish scale tissues of adjacent layers are staggered due to different laser scanning paths of each layer; the horizontal direction tissue is in a strip shape, the width of a single strip is 130-180 mu m, and the single strip is an extending track of the molten pool. Under the laser printing process parameters of the embodiment, the crystal grain structure is fine, uniform and densely distributed, and has no defects of air holes, looseness and inclusion. While AlFeCrCoNi is uniformly distributed in the matrix 2.1 The high-entropy alloy particles play a role in strengthening the second phase.
FIG. 3 shows the Al-based composite material (AlFeCrCoNi) prepared in this example 2.1 AlFeCrCoNi Single AlSi10 Mg) 2.1 EDS line scanning image of high-entropy alloy particles, wherein AlFeCrCoNi can be analyzed 2.1 The high-entropy alloy particles and the A1Si10Mg matrix form a distinct transition layer, the layer thickness of which is about 1 μm.
FIG. 4 shows the Al-based composite material (AlFeCrCoNi) prepared in this example 2.1 The EBSD spectrum of/AlSi 10 Mg), the grain size of the matrix is basically distributed between 2 and 6 mu m.
Example 2
The embodiment prepares the aluminum matrix composite material, and the specific process is as follows:
establishing a three-dimensional model of a workpiece, obtaining a plane profile model of each layer by slicing software, wiping parts such as a substrate, a powder cylinder, a scraper and the like by alcohol before a test, and filling argon into a forming cabin for protection, wherein the pressure in the forming cabin is kept at 5-8 kPa, and the oxygen content is lower than 100ppm.
95.5wt.% of AlSi10Mg alloy powder and 4.5wt.% of AlFeCrCoNi in terms of mass fraction 2.1 Adding high-entropy alloy particles into a ball milling tank, simultaneously filling inert gas into the ball milling tank, wherein the oxygen content in the tank is lower than 100ppm, simultaneously adding a bit of proportion of grinding balls into the tank, wherein the mass ratio of the grinding balls to powder is 1 2.1 a/AlSi 10Mg composite powder. Then a scraper is used for removing AlFeCrCoNi 2.1 the/AlSi 10Mg composite powder is scraped to a forming cabin from a powder cylinder, and an AlSi10Mg alloy substrate is flatly paved on the forming cabin to form a composite powder layer with the thickness of 30-35 mu m;
(2) And under the protection of Ar gas, performing laser scanning forming on the composite powder layer: in the process of printing and forming each layer, a laser beam forms an internal solid plane according to a scanning path preset according to a model, after the internal solid plane is formed, the laser beam sequentially carries out scanning and forming of an external outline from inside to outside around the edge of the internal solid plane of the layer, and then the single-layer printing process is completed. And executing the forming process of the printing layer by layer, after scanning one layer, driving the forming substrate to descend by one layer thickness height by the forming cabin, then spreading powder again, scanning and printing the laser again according to the next layer of model, and finally piling to obtain the aluminum-based composite material workpiece. Wherein, the laser scanning path of each layer forms an included angle of 60 degrees to 67 degrees with the laser scanning path of the previous layer until the AlFeCrCoNi is finished 2.1 Manufacturing and forming of the/AlSi 10Mg composite material. The laser power for printing the inner solid plane is consistent with the laser power for printing the outer contour, and the scanning speed for printing the inner solid plane is consistent with the scanning speed for printing the outer contour. The laser process parameters adopted in the embodiment are as follows: the laser power was 260W, the scanning speed was 1300mm/s, the scanning pitch was 130 μm, and the layer thickness was 30 μm.
Example 3
The embodiment prepares the aluminum matrix composite material, and the specific process is as follows:
establishing a three-dimensional model of a workpiece, obtaining a plane profile model of each layer by slicing software, wiping parts such as a substrate, a powder cylinder, a scraper and the like by alcohol before a test, and filling argon into a forming cabin for protection, wherein the pressure in the forming cabin is kept at 5-8 kPa, and the oxygen content is lower than 100ppm.
95.5wt.% of AlSi10Mg alloy powder and 4.5wt.% of AlFeCrCoNi in terms of mass fraction 2.1 Adding high-entropy alloy particles into a ball-milling tank, simultaneously filling inert gas into the ball-milling tank, wherein the oxygen content in the tank is lower than 100ppm, simultaneously adding a grinding ball with a certain proportion into the tank, wherein the mass ratio of the grinding ball to powder is 1 2.1 a/AlSi 10Mg composite powder. Then a scraper is used for removing AlFeCrCoNi 2.1 the/AlSi 10Mg composite powder is scraped to a forming cabin from a powder cylinder, and an AlSi10Mg alloy substrate is flatly paved on the forming cabin to form a composite powder layer with the thickness of 30-35 mu m;
(2) And under the protection of Ar gas, performing laser scanning forming on the composite powder layer: in the process of printing and forming each layer, the laser beam forms an internal solid plane according to a scanning path preset according to the model, and after the internal solid plane is formed, the laser beam sequentially scans and forms the external contour from inside to outside around the edge of the internal solid plane of the layer, so that the single-layer printing process is completed. And executing the forming process of the printing layer by layer, after scanning one layer, driving the forming substrate to descend by one layer thickness height by the forming cabin, then spreading powder again, scanning and printing the laser again according to the next layer of model, and finally piling to obtain the aluminum-based composite material workpiece. Wherein, the laser scanning path of each layer forms an included angle of 60 degrees to 67 degrees with the laser scanning path of the previous layer until the AlFeCrCoNi is finished 2.1 Manufacturing and forming of the/AlSi 10Mg composite material. The laser power for printing the internal solid plane is consistent with the laser power for printing the external contour, and the internal part is printedThe speed of scanning the solid plane is kept the same as the speed of scanning the printed outer contour. The laser process parameters adopted in the embodiment are as follows: the laser power was 300W, the scanning speed was 1200mm/s, the scanning pitch was 130 μm, and the layer thickness was 30 μm.
Comparative example
This comparative example prepared an AlSi10Mg alloy, which differs from example 2 in that no AlFeCrCoNi was added 2.1 The rest of the detailed process is carried out with reference to example 1.
FIG. 5 is an optical micrograph of the internal solid structure of the A1Si10Mg alloy prepared in the comparative example in the vertical (a) and horizontal (b) directions, macroscopically, the structure in the vertical direction is fish-scale, the individual cellular grains are distributed in layers, the diameter of the individual fish-scale structure is 50 μm to 120 μm, the fish scale structures of adjacent layers are staggered due to different laser scanning paths of each layer, the structure in the horizontal direction is a single strip, the width of the single strip is 120 μm to 150 μm, and the strip structure is a droplet rolling track or an extended track of a molten pool. FIG. 5 is a comparison of FIG. 2 with that of AlFeCrCoNi 2.1 The width of the melting channel behind the high entropy alloy particles is widened, which also indicates that AlFeCrCoNi 2.1 The addition of the high-entropy alloy particles is beneficial to the absorption of the laser energy by the AlSi10 Mg.
Test examples
The aluminum-based composite materials (AlFeCrCoNi) prepared according to the preparation methods in example 1, example 2, example 3 and comparative example 2.1 /AlSi10 Mg) and AlSi10Mg alloys were respectively prepared as standard tensile test specimens, and each specimen was respectively fixed to a material testing machine (electronic universal testing machine) to conduct a tensile test in a room temperature state, and the tensile test results are shown in table 1.
Table 1: alFeCrCoNi 2.1 Tensile strength and hardness of/AlSi 10Mg composite material and A1Si10Mg alloy
| Tensile strength (MPa) | Yield strength (MPa) | Hardness (HV) 0.5 ) | |
| Example 1 | 477 | 366 | 172 |
| Example 2 | 454 | 364 | 180 |
| Example 3 | 462 | 369 | 176 |
| Comparative example | 401 | 275 | 138 |
And (4) conclusion: as can be seen from Table 1, the AlFeCrCoNi prepared in examples 1 to 3 2.1 Compared with the conventional AlSi10Mg alloy manufactured by additive manufacturing, the strength of the AlSi10Mg composite material is obviously improved, specifically, the tensile strength is improved by about 19.3%, the yield strength is improved by about 33.1%, and the hardness is improved by about 26.8%.
The embodiments of the present invention have been described in detail, but the present invention is not limited to the embodiments, and various changes can be made without departing from the gist of the present invention within the knowledge of those skilled in the art. Furthermore, the embodiments of the present invention and the features of the embodiments may be combined with each other without conflict.
Claims (10)
1. An aluminum-based composite material characterized by containing an AlSi10Mg alloy and AlFeCrCoNi 2.1 High entropy alloy.
2. The aluminum-based composite material according to claim 1, wherein the AlFeCrCoNi is in the aluminum-based composite material 2.1 The content of the high-entropy alloy is 4.5-5 wt.%.
3. A method for preparing an aluminium matrix composite according to any one of claims 1 to 2, characterized in that it comprises the following steps:
s1: alSi10Mg alloy powder and AlFeCrCoNi 2.1 Ball-milling and mixing the high-entropy alloy particles to obtain AlFeCrCoNi 2.1 The method comprises the following steps of (1) paving composite powder/AlSi 10Mg on a substrate of a forming cabin of the SLM metal 3D printer to form a composite powder layer;
s2: under the protection of inert gas, carrying out laser scanning fusing and forming on the composite powder layer;
s3: and repeating the step S1 and the step S2 to realize layer-by-layer laser scanning, printing and forming to obtain the aluminum matrix composite.
4. The method according to claim 3, wherein the AlFeCrCoNi is in S1 2.1 The high-entropy alloy particles are spheroidal, and the average particle size is 13-53 mu m.
5. The production method according to claim 3, wherein the substrate in S1 is an Al-Si-based aluminum alloy plate.
6. The method according to claim 3, wherein the thickness of the composite powder layer in S1 is 30 to 35 μm.
7. The method according to claim 3, wherein the laser power of the laser scanning in S2 is 260W to 340W.
8. The manufacturing method according to claim 3, wherein a scanning speed of the laser scanning in S2 is 1200mm/S to 1300mm/S.
9. The preparation method according to claim 3, wherein the layer-by-layer laser scanning printing forming in S3 specifically comprises: the laser scanning path of each layer and the laser scanning path of the previous layer form an included angle of 60-67 degrees for printing and forming.
10. Use of the aluminium matrix composite according to any one of claims 1 to 2 in the manufacture of aeronautical, aerospace, automotive parts.
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