CN117051292B - High-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material and preparation method thereof - Google Patents
High-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material and preparation method thereof Download PDFInfo
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- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 81
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 79
- 239000002131 composite material Substances 0.000 title claims abstract description 78
- 238000002360 preparation method Methods 0.000 title abstract description 13
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 79
- HBMJWWWQQXIZIP-UHFFFAOYSA-N silicon carbide Chemical compound [Si+]#[C-] HBMJWWWQQXIZIP-UHFFFAOYSA-N 0.000 claims abstract description 65
- 229910010271 silicon carbide Inorganic materials 0.000 claims abstract description 65
- 239000011159 matrix material Substances 0.000 claims abstract description 58
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- 238000000034 method Methods 0.000 claims abstract description 28
- 230000002787 reinforcement Effects 0.000 claims abstract description 20
- 238000005266 casting Methods 0.000 claims abstract description 19
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- 238000007254 oxidation reaction Methods 0.000 claims description 17
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- 239000002994 raw material Substances 0.000 claims description 11
- 238000000498 ball milling Methods 0.000 claims description 9
- 229910052742 iron Inorganic materials 0.000 claims description 8
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 238000010438 heat treatment Methods 0.000 claims description 6
- 229910052710 silicon Inorganic materials 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 5
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- 229910052684 Cerium Inorganic materials 0.000 claims description 4
- 238000004140 cleaning Methods 0.000 claims description 4
- 229910052748 manganese Inorganic materials 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 230000004048 modification Effects 0.000 claims description 3
- 238000012986 modification Methods 0.000 claims description 3
- 229910052726 zirconium Inorganic materials 0.000 claims description 3
- 239000012535 impurity Substances 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims 3
- 239000000956 alloy Substances 0.000 abstract description 7
- 229910045601 alloy Inorganic materials 0.000 abstract description 5
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- 229910003336 CuNi Inorganic materials 0.000 description 10
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- 238000005054 agglomeration Methods 0.000 description 4
- 239000000155 melt Substances 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
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- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 3
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- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 1
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 1
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 1
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- 229910052727 yttrium Inorganic materials 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1005—Pretreatment of the non-metallic additives
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- C—CHEMISTRY; METALLURGY
- 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
- C22C32/0052—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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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F27—FURNACES; KILNS; OVENS; RETORTS
- F27D—DETAILS OR ACCESSORIES OF FURNACES, KILNS, OVENS, OR RETORTS, IN SO FAR AS THEY ARE OF KINDS OCCURRING IN MORE THAN ONE KIND OF FURNACE
- F27D27/00—Stirring devices for molten material
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Composite Materials (AREA)
- General Engineering & Computer Science (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
Abstract
The invention relates to the technical field of alloy materials, in particular to a high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material and a preparation method thereof, wherein the high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material comprises a silicon carbide particle reinforcement and an aluminum alloy matrix, the mass of the silicon carbide particle reinforcement accounts for 5% -35% of the total mass of the aluminum-based composite material, alloy elements with lower price are selected, the content and the proportion of the alloy elements are controlled, the particle reinforcement are pretreated, the high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material is prepared by adopting a gravity casting method, the high-temperature performance of the prepared composite material is obviously improved, and the high-temperature-resistant wear-resistant thermal fatigue-resistant composite material has excellent high-temperature-resistant wear-resistant fatigue performance under the service condition of 350 ℃.
Description
Technical Field
The invention relates to the technical field of alloy materials, in particular to a high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material and a preparation method thereof.
Background
With the development of modern science and technology and manufacturing industry, the requirements on the mechanical properties of metal materials are higher and higher, and aluminum-based composite materials are paid attention to in the fields of automobiles, aerospace and the like due to the advantages of low density, wear resistance, good fatigue resistance and the like. The aluminum-based composite material is widely applied to manufacturing of aluminum-based composite materials of engine pistons, brake discs and the like, the industry is higher and higher in high-temperature resistance, wear resistance and thermal fatigue resistance, and the performance of the aluminum-based composite materials which are widely used at present is difficult to fully meet the use requirement at the temperature of more than 350 ℃. There are a great deal of researches on high-strength wear-resistant aluminum-based composite materials at home and abroad, and improvement is usually carried out on preparation technology, for example, high-cost technology such as powder metallurgy, aluminum liquid infiltration, pressure casting and the like is adopted to improve the performance of the composite materials. The traditional gravity casting can greatly reduce the production cost, but under the gravity casting condition, the problems of insufficient interface combination, poor dispersibility, easy agglomeration and the like exist in the ubiquitous reinforcement of the aluminum-based composite material and the aluminum alloy interface, and the problems greatly destroy the performance of the aluminum-based composite material and limit the application of the aluminum-based composite material. Or may add alloying elements to the aluminum alloy matrix, such as: the contents of elements such as Cu, ni and the like are increased to improve the mechanical properties, zr, ti, V and rare earth elements are added to improve the structure morphology, and specific alloy components can be adjusted according to the practical properties.
Disclosure of Invention
The invention provides a preparation method of a high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material, and provides a high-temperature-resistant wear-resistant thermal fatigue-resistant aluminum-based composite material which is tightly combined with an aluminum alloy matrix and has good high-temperature-resistant wear-resistant thermal fatigue-resistant performance aiming at a gravity casting process. The method realizes that a plurality of high-temperature stable phases which are uniformly and dispersedly distributed are independently separated out in the aluminum-based composite material, simplifies the preparation process of the aluminum-based composite material, and is beneficial to large-scale preparation and application of certain special-purpose aluminum-based composite materials.
The aim of the invention is achieved by the following technical scheme:
the high temperature resistant, wear resistant and thermal fatigue resistant aluminum-based composite material comprises 15-35% of SiC particle reinforcement by mass percent based on the total mass of the aluminum-based composite material, and the balance of an aluminum alloy matrix;
wherein, the aluminum alloy matrix comprises the following components: the aluminum alloy comprises the following components in percentage by mass based on the total mass of an aluminum alloy matrix: 9 to 12 percent of Si, 1 to 2.5 percent of Cu, 1 to 2 percent of Ni, 0.2 to 1.5 percent of Mg, 1.5 to 2.5 percent of Mn, 0.5 to 1.5 percent of Cr, 0.3 to 0.8 percent of Fe, 0.01 to 0.5 percent of Zr, 0.25 percent of Ce, 0.25 percent of La, 0.3 percent of V, 0.3 percent of Y, 0.4 percent of Ti, 0.04 percent of Sr, and 0.01 percent of B; the balance Al and unavoidable impurities.
Further, the aluminum alloy is hypoeutectic aluminum-silicon alloy.
In the aluminum-based composite material, hypoeutectic silicon with better castability and thermal stability is adopted, and meanwhile, the lower Si content is convenient for introducing additional silicon carbide.
Further, according to the mass percentage, the following elements are satisfied:
in the method, in the process of the invention,is the mass percent of Ni in the aluminum alloy matrix, < >>Is Cu mass percent in the aluminum alloy matrix, < >>Is the mass percent of Mg in the aluminum alloy matrix, < >>Is the mass percent of Mn in the aluminum alloy matrix, < >>The mass percentage of Cr in the aluminum alloy matrix is as follows.
Through the component design, the precipitated phase with good high-temperature mechanical property can be obtained to the maximum.
Further, the aluminum alloy comprises Al 3 CuNi phase, said Al 3 The volume fraction of the CuNi phase is not less than 6%.
Cu and Ni elements are introduced to strengthen the aluminum-silicon alloy, and Al is generated by introducing Cu elements 2 Cu、Al 5 Cu 2 Mg 8 Si 6 Metastable phase, however, the increase of Cu content causes the shrinkage of solidification volume and the increase of air holes, so that the mechanical property is deteriorated, and the Cu element content is controlled to be less than 2.5.
Ni element introduction will first generate Al 7 Cu 4 Ni、Al 3 CuNi phase, further increasing Ni content, will generate Al 3 Ni phase, above three Ni-rich phases, al 3 CuNi phaseThe heat stability and fatigue resistance of the present invention are optimized, and thus, the present invention controls 0.5<Ni/Cu<0.7 in order to obtain more Al 3 A CuNi phase.
Further, in the aluminum alloy, according to the mass percentage,
when the mass of the silicon carbide particle reinforcement accounts for 5% -15% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 0.2 to 0.7 percent of the mass of the aluminum alloy matrix.
When the mass of the silicon carbide particle reinforcement accounts for 15% -30% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 0.7-1.5% of the mass of the aluminum alloy matrix.
When the mass of the silicon carbide particle reinforcement accounts for 30% -50% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 1.5-2% of the mass of the aluminum alloy matrix.
The aluminum alloy comprises Al 5 Cu 2 Mg 8 Si 6 A phase of Al 3 The volume fraction of the CuNi phase is 6.5% -7.4%.
The Mg element can improve the wettability of the aluminum alloy matrix and the silicon carbide interface, a part of Mg exists at the interface of the silicon carbide particles and the aluminum matrix, and a part of Mg exists in the form of intermetallic compounds. In the intermetallic compound, mg is preferentially selected from Al 5 Cu 2 Mg 8 Si 6 Phase precipitation, which occurs as the content of Mg increases 2 Si phase, mg 2 The strengthening mechanism of Si phase in the aluminum-silicon matrix is mainly Orowan strengthening, and the material plasticity is seriously reduced while the room temperature strength is improved.
Therefore, according to the invention, when the percentage of SiC is 5 to 15 percent, the percentage of Mg is 0.2 to 0.5 percent; 15 to 30 percent of SiC and 0.5 to 1.2 percent of Mg; siC:>at 30%, 1.2% -2% of Mg to control the existence form of Mg element. And controlProper amount of Cu content is reduced, mg content is increased, and Al can be reduced 2 Cu and Mg 2 Si phase is generated to convert Cu and Mg elements into Al with better creep resistance 5 Cu 2 Mg 8 Si 6 And (3) phase (C).
Further, the aluminum alloy comprises dendritic Al 15 (Mn,Fe) 3 Si 2 And (3) phase (C). And Al is 15 (Mn,Fe) 3 Si 2 The grain size is about 20 um. Al (Al) 15 (Mn,Fe) 3 Si 2 The phase and the eutectic silicon matrix form a three-dimensional net structure.
Mn element is added to generate two-dimensional lath Al 13 Mn 4 Si 8 Lath-shaped Al 13 Mn 4 Si 8 Further generating dendritic Al through peritectic reaction 15 Mn 3 Si 2 Phases, dendritic Al 15 Mn 3 Si 2 The high temperature stability and fatigue resistance of the phase are better. To improve Mn-rich phase, proper amount of Fe element is added to promote lath Al 13 Mn 4 Si 8 Conversion to dendritic Al 15 (Mn,Fe) 3 Si 2 . With the increase of Mn content, the size of Mn-rich phase increases to 50-80 um level, but the excessive precipitated phase easily damages the mechanical property of the material, the invention controls 1.5<Mn/Cr<2 because Cr element may be present in the Mn-rich phase and refine the Mn-rich phase to around 20 um.
Al 15 (Mn,Fe) 3 Si 2 Is attached to Al 7 CuNi phase, al 3 The CuNi phase is separated out, a three-dimensional network structure is formed by the CuNi phase and the eutectic silicon matrix, and the network structure is further reinforced by the silicon carbide particle reinforcement, so that the critical stress of crack initiation is improved. The separated hard phase and ceramic particles are used as hard supporting points in the friction process, so that the hard supporting points are not easy to abrade, an Al matrix is protected, and the friction performance of the material is improved.
Further, in the aluminum alloy, the following elements in percentage by mass are as follows:. In (1) the->Is the mass percentage of Zr in the aluminum alloy matrix,is in an aluminum alloy matrixMass percent of Ce, europe>Is the mass percentage of La in the aluminum alloy matrix, < >>Is the mass percentage of V in the aluminum alloy matrix, < >>Is the mass percentage of Y in the aluminum alloy matrix.
In the invention, the addition of Zr element can form Al 3 Zr phase, and grain is obviously refined; the Sr element is added in the form of Al-10Sr, clusters at Si liquid interfaces in the modified alloy are formed, the eutectic Si morphology is improved, and the strength and the plasticity of the material are improved; b is added in the form of Al-5Ti-B, and has remarkable effect on grain refinement of Al-Si alloy; part of Ti element exists in the additionally added refiner Al-5Ti-B, and the other part of Ti exists in the high-temperature stable phase Ti 2 Al 20 Ce, ce.
Further, in the aluminum-based composite material, the silicon carbide is subjected to high-temperature oxidation pretreatment, the particle size of the silicon carbide is 10-40 mu m, and the purity of the silicon carbide is more than 99.7%. Specifically, firstly cleaning silicon carbide, then performing low-energy ball milling and mechanical stirring oxidation, and then sieving.
Firstly, selecting silicon carbide particles with the particle diameter of 5-60 mu m and the purity of more than 99%, and more preferably selecting particles with the particle diameter of 10-40 mu m and the purity of more than 99.7%. And soaking for 24-36 hours by adopting hydrofluoric acid, stirring in the process, and washing to be neutral after soaking to obtain the slurry.
Then ball milling is carried out on the silicon carbide slurry by adopting a horizontal low-energy ball mill, the silicon carbide slurry and silicon carbide grinding balls are put into a nylon grinding tank, and the volume ratio of the silicon carbide to the grinding balls is 1:1-3; and (3) injecting deionized water to 2/5~4/5 of the volume of the grinding tank, starting the ball mill to start ball milling, wherein the rotating speed of the ball mill is 100-300 r/min, and the ball milling time is 5-30 h. And after ball milling, taking out the slurry, and drying at 100-300 ℃.
In the prior art, high-energy ball milling is generally adopted to optimize the shape of the silicon carbide particles, and the silicon carbide particles are easily cracked in the mode, so that sharp corners appear, and the silicon carbide is difficult to be effectively passivated and rounded. Therefore, the invention adopts the nylon grinding tank and the silicon carbide grinding balls to carry out low-energy ball milling, and optimizes the shape of the silicon carbide particles and avoids the cracking of the particles by combining with an adaptive grinding process.
And (3) placing the ball-milled silicon carbide in an oxidation tube for oxidation, wherein the oxidation temperature is 800-1300 ℃, the oxygen flow is 0.1-0.8L/min, the oxidation time is 1-8 h, and the whole process of the oxidation is mechanically stirred by adopting a stirring paddle, the stirring speed is 5-50 r/min, so that particle adhesion or uneven oxidation is prevented. And naturally cooling and vibrating and screening after the oxidation is finished so as to further prevent the particles from adhering and agglomerating.
The high-temperature stirring oxidation mode can avoid the adhesion and agglomeration of particles which are easy to generate in the existing calcination oxidation. And through stirring particles in the oxidation process and controlling the oxygen introducing amount, the oxidation modification of the silicon carbide surface is effectively realized, and the generated oxide film is uniform and has proper thickness, so that the wettability in stirring casting and the interface strength in the aluminum-based composite material are further improved.
The preparation method of the aluminum-based composite material adopts a casting method. In the prior art, the preparation method of the aluminum-based composite material mainly comprises three methods of casting, powder metallurgy and aluminum liquid infiltration. Compared with powder metallurgy and infiltration, the casting method has the advantages of simple equipment, low production cost, contribution to industrial production and the like, and the aluminum-based composite material prepared by the casting method occupies more than 40 percent of the total amount of the aluminum-based composite material. The stirring casting process is also called stirring composite process, and is characterized by that the reinforcing body is mixed with liquid aluminium alloy matrix by means of mechanical stirring device, then the aluminium alloy matrix is made into cast ingot or component of aluminium base composite material by means of normal pressure casting or vacuum pressure casting or pressure casting, and its advantages are that it adopts conventional smelting equipment, and its cost is low, so that it can prepare precise complex component structure. However, some problems still remain to be solved when preparing the silicon carbide reinforced aluminum-based composite material by stirring and casting, such as: casting defects (mixing of gas and inclusions), uneven particle distribution, and the like. According to the method, a vacuum transition variable speed stirring casting method is adopted, after silicon carbide is added into an aluminum alloy melt, the formation of irregular vortex in the melt is promoted by adopting multi-frequency transition variable speed stirring, and the agglomeration of the silicon carbide is further dispersed so as to promote the distribution of the silicon carbide.
The method comprises the following steps:
(1) Preparing raw materials: preparing component raw materials of an aluminum alloy matrix, and cleaning;
(2) Pretreatment of silicon carbide: carrying out low-energy ball milling and high-temperature oxidation pretreatment on silicon carbide particles;
(3) Preparing an aluminum melt: placing an aluminum alloy raw material in a crucible, vacuumizing, and heating to melt to obtain an aluminum alloy melt;
(4) Adding silicon carbide: adding silicon carbide into the aluminum alloy melt in the process of stirring the aluminum alloy melt to obtain an aluminum-based composite material melt;
(5) Vacuum transition variable speed stirring: further vacuumizing, and thoroughly scattering silicon carbide particles through transition variable speed stirring;
(6) Modification and refinement: adding a refiner and an alterant into the prepared aluminum-based composite material melt;
(7) Casting: heating, pouring the aluminum-based composite material melt into a preheated die, and cooling and forming to obtain an ingot.
Preferably, the aluminum alloy in the step (1) is an alloy component of the present invention. And ultrasonically cleaning the raw materials by using acetone or absolute ethyl alcohol for 10-30 minutes.
Preferably, the specific steps of the step (3) are as follows: and (3) placing the raw materials into a vacuum induction melting furnace crucible with a stirring device, vacuumizing to 50-150 Pa, heating to 700-800 ℃, and preserving heat for 0.5-1 h to ensure that all the raw materials are completely melted.
Preferably, the specific steps of the step (4) are as follows: and (3) reducing the temperature of the melt to a semi-solid temperature range, inserting a stirring head below the liquid level, starting a stirring device to stir at a constant speed, wherein the rotating speed is 300-800 r/min, and adding silicon carbide into the central vortex of the aluminum alloy melt through a secondary feeding device. Further preferably, the semi-solid temperature is 10-30 ℃ above the solidus of the aluminum alloy matrix.
Preferably, the specific steps of the step (5) are as follows: after the silicon carbide is added, vacuumizing to 30-50 Pa, increasing the rotating speed to 800-2000 r/min, and continuously stirring for 1-3 h in a semi-solid temperature interval. And (3) carrying out transition variable speed stirring for 10-30 times, wherein the rotating speed transition difference value is 300-1500 r/min, and the speed transition is completed within 1-3 s.
The silicon carbide is mixed and dispersed in the aluminum alloy melt in a transition variable speed stirring mode. In the prior art, a stirring mode with constant rotation speed is generally adopted, and after the stirring mode is adopted for a period of time, a stable vortex flow field is formed by the melt, so that the partially agglomerated silicon carbide particles are difficult to break up under the stable flow field, and the dispersing effect is poor. Therefore, in order to solve the problems, the invention adopts a transition variable speed stirring mode, and the main idea is that in the stirring process, the stirring rotating speed is enabled to have acceleration higher than a certain critical value, and the acceleration of the rotating speed can form a large shearing force in melt vortex, so that the instability of the original steady-state vortex is facilitated, and further, the agglomerated silicon carbide particles rotating along with the vortex are scoured and scattered, thereby facilitating the uniform distribution of the silicon carbide particles.
Preferably, the refiner and modifier used in the step (6) are 0.1-0.5 wt.% of Al-5Ti-B and 0.1-0.4 wt.% of Al-10Sr, respectively. And before adding the thinning modifier, reducing the stirring rotation speed to 200-300 r/min, and increasing the temperature of the aluminum-based composite material melt to 700-720 ℃. And (5) after adding the refiner and the modifier, preserving heat for 10-20 min.
Preferably, the specific steps of the step (7) are as follows: and raising the temperature of the aluminum-based composite material melt to 730-750 ℃, pouring the aluminum-based composite material melt into a die with the preheating temperature of 200-300 ℃, and cooling and forming to obtain an aluminum-based composite material ingot.
Further, the aluminum-based composite material satisfies the following conditions under the as-cast condition: the tensile strength at 300 ℃ is more than or equal to 170 Mpa, and the tensile strength at 350 ℃ is more than or equal to 150Mpa.
The beneficial effect for prior art is for this application:
1. the aluminum-based composite material prepared by the method does not contain precious and rare elements, the metastable phase generation is reduced in the aluminum-based composite material by controlling the content and the proportion of the elements, a large amount of high-temperature stable phase is introduced, a firm three-dimensional network structure is formed by the aluminum-based composite material and the co-crystal silicon matrix, the high-temperature stability of the material is improved under the condition of maintaining certain room-temperature plasticity, and the characteristics of low cost and easiness in addition are beneficial to industrial production.
2. The silicon carbide pretreatment process adopts a low-energy ball milling and high-temperature stirring oxidation method, so that the shape of silicon carbide particles is effectively improved, mutual adhesion agglomeration among the particles is prevented, and interface combination of silicon carbide and an aluminum alloy matrix is enhanced.
3. The aluminum-based composite material has the performances of wear resistance, high temperature resistance, thermal fatigue resistance and the like.
Drawings
Fig. 1 is a metallographic structure diagram in example 1 of the present application.
Fig. 2 is an SEM image in example 1 of the present application.
Fig. 3 is an EDS diagram in example 1 of the present application.
Fig. 4 is a thermal fatigue crack in example 1 of the present application.
Detailed Description
The technical solution of the present invention will be further described in detail below with reference to the accompanying drawings and examples of the present invention, which are clearly illustrated by way of example and not by way of limitation. The specific conditions are not noted in the examples and are carried out according to conventional conditions or conditions recommended by the manufacturer. The reagents or apparatus used were conventional products commercially available without the manufacturer's attention.
Example 1:
an aluminum-based composite material, wherein the weight of SiC particle powder is 25%, and the weight of aluminum alloy is as follows: 9% of Si, 2.5% of Cu, 1.5% of Ni, 0.6% of Mg, 1.5% of Mn, 0.6% of Cr, 0.4% of Fe, 0.2% of Zr, 0.1% of Ce, 0.1% of La, 0.1% of V, 0.1% of Y, 0.15% of Ti, 0.01% of Sr and 0.01% of B.
The preparation method of the aluminum alloy comprises the following steps: the above raw materials were ultrasonically cleaned with acetone for 15 minutes. Placing raw materials into a vacuum induction melting furnace crucible with a stirring deviceVacuumizing to 50 Pa, heating to 700 ℃, preserving heat for 0.5h, reducing the temperature of the melt to a semi-solid temperature interval, inserting a stirring head below the liquid level, starting a stirring device to stir at a constant speed, wherein the rotating speed is 600r/min, and adding silicon carbide into the central vortex of the aluminum alloy melt through a secondary feeding device. Further preferably, the semi-solid temperature is 20 ℃ above the solidus of the aluminum alloy matrix. After the silicon carbide is added, vacuumizing to 50 Pa, increasing the rotating speed to 1000r/min, and continuously stirring for 2 hours in a semi-solid temperature interval. During the stirring, 20 times of transition speed change stirring are carried out, the rotating speed transition difference value is 800r/min, and the used refiner and modifier are respectively 0.3 wt percent of Al-5Ti-B and 0.1 wt percent of Al-10Sr. Before adding the thinning modifier, the stirring speed is reduced to 200r/min, and the temperature of the aluminum-based composite material melt is increased to 700 ℃. Adding refiner and modifier, and maintaining the temperature for 15min. Raising the temperature of the aluminum-based composite material melt to 730 ℃, pouring the aluminum-based composite material melt into a die with the preheating temperature of 200 ℃, and cooling and forming to obtain an aluminum-based composite material cast ingot. The metallographic structure is shown in figure 1, the distribution of SiC particles in an aluminum alloy matrix is relatively uniform, no obvious SiC aggregation exists, and the porosity is low. As shown in FIG. 2, the Cr element modifies Mn-rich phase and off-white Al 15 (Mn,Cr,Fe) 3 Si 2 The phase is precipitated in a block shape, the size is reduced to 20-50 mu m, and the Al is bright white 3 CuNi phase is arrow-shaped and strip-shaped, is mainly attached to SiC particles to separate out, and a small amount of Mg element is gray Al 5 Cu 2 Mg 8 Si 6 And (3) phase precipitation. The content of the elements in the different phases is shown in fig. 3 and table 1.
Table 1 content (wt.%) of each element in different spectra
The aluminum-based composite ingot prepared in the embodiment has a tensile strength of 370MPa at room temperature, an elongation of 1.5% at room temperature, a tensile strength of 175MPa at 300 ℃ and a tensile strength of 155MPa at 350 ℃. The thermal fatigue test shows excellent thermal fatigue resistance, and after the thermal fatigue test is repeated for 450 times at 30-250 ℃, the prefabricated notch still does not generate obvious thermal fatigue crack, as shown in figure 4.
Example 2:
an aluminum-based composite material, siC particle powder is 30% by weight, and an aluminum alloy comprises the following components by weight: 10% of Si, 2% of Cu, 1.5% of Ni, 0.5% of Mg, 2% of Mn, 1% of Cr, 0.5% of Fe, 0.02% of Zr, 0.03% of Ce, 0.1% of La, 0.02% of V and 0.1% of Y; 0.15% of Ti, 0.01% of Sr and 0.01% of B.
The preparation method of the aluminum alloy is the same as in example 1.
The aluminum-based composite ingot prepared in the embodiment has a tensile strength of 365MPa at room temperature, an elongation of 1.6% at room temperature, a tensile strength of 169MPa at 300 ℃ and a tensile strength of 150MPa at 350 ℃.
Example 3:
an aluminum-based composite material, siC particle powder is 30% by weight, and an aluminum alloy comprises the following components by weight: 11% of Si, 1.5% of Cu, 1% of Ni, 0.5% of Mg, 2% of Mn, 1% of Cr, 0.5% of Fe, 0.3% of Zr, 0.03% of Ce, 0.1% of La, 0.02% of V and 0.1% of Y; 0.15% of Ti, 0.01% of Sr and 0.01% of B.
The preparation method of the aluminum alloy is the same as in example 1.
The aluminum-based composite ingot prepared in the embodiment has the tensile strength of 382Mpa at room temperature, the elongation at room temperature of 1.3%, the tensile strength of 178 Mpa at 300 ℃ and the tensile strength of 165Mpa at 350 ℃.
The foregoing description is only exemplary embodiments of the present application and is not intended to limit the scope of the present application, and all equivalent structures or equivalent processes using the descriptions and the drawings of the present application, or direct or indirect application in other related technical fields are included in the scope of the present application.
Claims (9)
1. A high temperature resistant wear resistant thermal fatigue resistant aluminum matrix composite is characterized in that: the aluminum-based composite material comprises a silicon carbide particle reinforcement and an aluminum alloy matrix, wherein the mass of the silicon carbide particle reinforcement accounts for 5% -35% of the total mass of the aluminum-based composite material;
wherein, each element composition in the aluminum alloy matrix is as follows: the mass percent of each element is as follows, calculated by the mass percent of the aluminum alloy matrix being 100 percent: 9 to 12 percent of Si, 1 to 2.5 percent of Cu, 1 to 2 percent of Ni, 0.2 to 1.5 percent of Mg, 1.5 to 2.5 percent of Mn, 0.5 to 1.5 percent of Cr, 0.3 to 0.8 percent of Fe, 0.01 to 0.5 percent of Zr, 0.03 to less than or equal to Ce <0.25 percent, 0.1 to less than or equal to La <0.25 percent, 0.02 to less than or equal to V <0.3 percent, 0.1 to less than or equal to Y <0.3 percent, 0.15 to less than or equal to Ti <0.4 percent, 0.01 to less than or equal to Sr <0.04 percent, and 0.01 percent of B; the balance Al and unavoidable impurities.
2. The aluminum-based composite material according to claim 1, wherein the aluminum alloy matrix composition meets:
in the method, in the process of the invention,is the mass percent of Ni in the aluminum alloy matrix, < >>Is the mass percentage of Cu in the aluminum alloy matrix,is the mass percent of Mg in the aluminum alloy matrix, < >>Is the mass percent of Mn in the aluminum alloy matrix, < >>The mass percentage of Cr in the aluminum alloy matrix is as follows.
3. The aluminum-based composite material according to claim 1, wherein the aluminum alloy matrix composition meets:
in the method, in the process of the invention,is the mass percent of Zr in the aluminum alloy matrix, < >>Is the mass percent of Ce in the aluminum alloy matrix,is the mass percentage of La in the aluminum alloy matrix, < >>Is the mass percentage of V in the aluminum alloy matrix, < >>Is the mass percentage of Y in the aluminum alloy matrix.
4. The aluminum-based composite material according to claim 1, wherein the silicon carbide particle reinforcement accounts for 5-15% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 0.2 to 0.7 percent of the mass of the aluminum alloy matrix.
5. The aluminum-based composite material according to claim 1, wherein the silicon carbide particle reinforcement accounts for 15-30% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 0.7-1.5% of the mass of the aluminum alloy matrix.
6. The aluminum-based composite material according to claim 1, wherein the silicon carbide particle reinforcement accounts for 30% -50% of the total mass of the aluminum-based composite material; in the aluminum alloy matrix, the mass of Mg element accounts for 1.5-2% of the mass of the aluminum alloy matrix.
7. The aluminum-based composite material according to claim 1, wherein the silicon carbide particle reinforcement is subjected to high temperature oxidation pretreatment, the size of the silicon carbide particle reinforcement is 10-40 μm, and the purity is more than 99.7%.
8. The aluminum-based composite material according to claim 1, wherein the tensile strength of the aluminum-based composite material in an as-cast state is equal to or more than 170 Mpa at 300 ℃ and equal to or more than 150Mpa at 350 ℃.
9. The method for producing an aluminum-based composite material according to any one of claims 1 to 8, comprising the steps of:
(1) Preparing raw materials: preparing component raw materials of an aluminum alloy matrix, and cleaning;
(2) Pretreatment of silicon carbide: carrying out low-energy ball milling and high-temperature oxidation pretreatment on the silicon carbide particles to obtain a silicon carbide particle reinforcement;
(3) Preparing an aluminum melt: placing an aluminum alloy raw material in a crucible, vacuumizing, and heating to melt to obtain an aluminum alloy melt;
(4) Adding silicon carbide particle reinforcement: adding silicon carbide particle reinforcement into the aluminum alloy melt in the process of stirring the aluminum alloy melt to obtain an aluminum-based composite material melt;
(5) Vacuum transition variable speed stirring: further vacuumizing, and thoroughly scattering the silicon carbide particle reinforcement through transition variable speed stirring;
(6) Modification and refinement: adding a refiner and an alterant into the prepared aluminum-based composite material melt;
(7) Casting: heating, pouring the aluminum-based composite material melt into a preheated die, and cooling and forming to obtain an ingot.
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