CN112626378A - Iron-aluminum alloy composite reinforced aluminum-based material, and preparation method and application thereof - Google Patents
Iron-aluminum alloy composite reinforced aluminum-based material, and preparation method and application thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
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- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/74—Methods of treatment in inert gas, controlled atmosphere, vacuum or pulverulent material
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- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/008—Heat treatment of ferrous alloys containing Si
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- C22C33/00—Making ferrous alloys
- C22C33/02—Making ferrous alloys by powder metallurgy
- C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
- C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/02—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working in inert or controlled atmosphere or vacuum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C24/00—Coating starting from inorganic powder
- C23C24/08—Coating starting from inorganic powder by application of heat or pressure and heat
- C23C24/10—Coating starting from inorganic powder by application of heat or pressure and heat with intermediate formation of a liquid phase in the layer
- C23C24/103—Coating with metallic material, i.e. metals or metal alloys, optionally comprising hard particles, e.g. oxides, carbides or nitrides
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- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16D—COUPLINGS FOR TRANSMITTING ROTATION; CLUTCHES; BRAKES
- F16D65/00—Parts or details
- F16D65/02—Braking members; Mounting thereof
- F16D65/12—Discs; Drums for disc brakes
- F16D65/125—Discs; Drums for disc brakes characterised by the material used for the disc body
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/04—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling
- B22F2009/043—Making metallic powder or suspensions thereof using physical processes starting from solid material, e.g. by crushing, grinding or milling by ball milling
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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
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
- Y02T30/00—Transportation of goods or passengers via railways, e.g. energy recovery or reducing air resistance
Abstract
The application relates to an iron-aluminum alloy composite reinforced aluminum-based material, a preparation method and application thereof. The material comprises an aluminum-based alloy layer and Fe metallurgically bonded with the aluminum-based alloy layer3Al alloy layer and Fe3FeAl alloy layer metallurgically bonded with Al alloy layer, Fe3The Al alloy layer is mainly made of Fe3Al phase and ZrB2The FeAl alloy layer mainly consists of a FeAl phase, a B phase and Al2O3Phase composition. The iron-aluminum alloy composite reinforced aluminum-based material not only has excellent high-temperature mechanical property, corrosion resistance and wear resistance of an iron-aluminum intermetallic compound, but also keeps the advantages of high thermal conductivity, light weight and the like of an aluminum-based alloy. The material is used as a brake disc material for high-speed rail transit, so that the production cost can be greatly reduced, the service temperature of the brake disc can be remarkably improved, and the service life of the brake disc can be remarkably prolonged.
Description
Technical Field
The invention relates to a multilayer surface composite reinforced aluminum-based material, in particular to an iron-aluminum alloy composite reinforced aluminum-based material, and a preparation method and application thereof.
Background
With the increasing severity of the traffic jam problem, urban rail transit has become a necessary development trend for solving the urban traffic problem due to the characteristics of large traffic volume, rapidness, comfort, energy conservation, environmental protection and the like. With the continuous progress of the transportation technology, the design speed of the urban rail transit vehicle is higher and higher, which is improved from 80km/h to 120km/h in the past, and higher requirements are also put forward on the safety braking performance of the vehicle. The braking of the vehicle is substantially to convert the kinetic energy of the train into heat energy by using a friction pair so as to achieve the purposes of speed reduction and stopping, and the heat is dissipated by heat exchange with the external environment, so that the heat resistance strength and the heat dissipation capacity of a brake disc are one of key indexes for measuring the braking performance of the vehicle.
In addition, with the continuous expansion of urban rail transit construction scale and the continuous increase of operation networks, the energy consumption is also greatly increased. According to statistics, the traction energy consumption accounts for about 30% of the total energy consumption, the vehicle mass is reduced by 10%, the traction energy consumption can be reduced by about 6%, the vehicle braking device accounts for about 20% of the unsprung weight, most of the 20% is occupied by the brake disc, therefore, the light brake disc can play a remarkable weight reduction effect, the speed can be increased, the noise can be reduced, the energy consumption and the carbon emission can be reduced, the wheel rail abrasion can be reduced, the maintenance cost of a rail line can be reduced, and therefore huge social and economic benefits are brought.
The aluminum-based alloy has the characteristics of small density, high specific strength, low thermal expansion coefficient, easy processing and the like, has better plasticity, electric conduction, heat conduction, corrosion resistance, weldability and mechanical properties, is often used for replacing traditional brake disc materials such as iron and steel in recent years, and becomes the main research direction of light weight of the rail transit vehicles at present. However, the problems of poor high-temperature mechanical properties, poor frictional wear resistance and poor high-temperature oxidation resistance inherent in aluminum-based alloys limit the further use of the aluminum-based alloys under the braking condition of high-speed rail transit. At present, a reinforcing phase is adopted to reinforce an aluminum-based material so as to improve the performances of wear resistance, damage resistance and the like, but with the addition of the reinforcing phase, the preparation difficulty and the manufacturing cost are increased, and the high-temperature mechanical property of the material cannot meet the use requirement of high-speed rail transit braking. Currently, technologists adopt surface modification methods such as carburizing, nitriding, spraying, micro-arc oxidation, electroplating, ion plating, physical vapor deposition, chemical vapor deposition, ion implantation, plasma immersion ion implantation and deposition and the like to form various types of functional films or coatings on the surface of the aluminum-based alloy. However, these methods generally have the problems of high cost, thin film or coating thickness and poor bonding strength with aluminum-based alloys. Therefore, it is not suitable for the working conditions of high temperature and large stress under the condition of high-speed braking. In order to make up for the above disadvantages, people begin to adopt a laser cladding technology of a functional composite coating with controllable coating thickness and capable of forming good metallurgical bonding with the surface of a base material, so that the comprehensive properties of the surface of the aluminum-based alloy, such as hardness, wear resistance, corrosion resistance, oxidation resistance, and the like, are remarkably improved.
The iron-aluminum intermetallic compound has excellent high-temperature oxidation resistance and sulfidization resistance, relatively low density, low price and the like, and can be used as a corrosion-resistant, high-temperature-resistant and oxidation-resistant reinforced protective layer on the surface of the aluminum-based alloy. However, the mismatch of the thermophysical properties of the laser cladding powder and the substrate easily causes the coating to have defects such as cracks, which is fatal in the application of brake discs.
Disclosure of Invention
Based on the above, there is a need for a crack-free iron-aluminum alloy composite reinforced aluminum-based material which is in good metallurgical bonding with an aluminum-based alloy, and which not only has excellent high-temperature mechanical properties, corrosion resistance and wear resistance of an iron-aluminum intermetallic compound, but also retains the advantages of high thermal conductivity, light weight and the like of the aluminum-based alloy. The material is used as a brake disc material for high-speed rail transit, so that the production cost can be greatly reduced, the service temperature of the brake disc can be remarkably improved, and the service life of the brake disc can be remarkably prolonged.
An iron-aluminum alloy composite reinforced aluminum-based material comprises an aluminum-based alloy layerFe metallurgically bonded to said aluminium-based alloy layer3Al alloy layer and Fe3A FeAl alloy layer metallurgically bonded with the Al alloy layer, the Fe3The Al alloy layer is mainly made of Fe3Al phase and ZrB2The FeAl alloy layer mainly consists of a FeAl phase, a B phase and Al2O3And (4) forming.
In one embodiment, the FeAl alloy layer further comprises MoSi2And (4) phase(s).
In addition, the application also provides a preparation method of the iron-aluminum alloy composite reinforced aluminum-based material, which comprises the following steps:
in protective gas atmosphere, ball milling and mixing Fe powder, Al powder, amorphous B powder and Zr powder according to proportion to obtain Fe3Al alloy raw material powder;
in protective gas atmosphere, Fe powder, Al powder, amorphous B powder and Al powder2O3Ball-milling and mixing the particles according to a proportion to obtain FeAl alloy raw material powder;
subjecting said Fe to3Al alloy raw material powder is laid on the surface of the aluminum-based alloy, and is annealed after laser cladding in protective gas atmosphere to obtain metallurgically bonded Fe3An Al alloy layer and an Al alloy layer;
laying the FeAl alloy raw material powder on the Fe3And carrying out laser cladding on the surface of the Al alloy layer in a protective gas atmosphere and then annealing to obtain the iron-aluminum alloy composite reinforced aluminum-based material.
In one embodiment, the Fe3In the Al alloy raw material powder, the mass ratio of the Fe powder to the Al powder is (4-7): 1, and the mass of the amorphous B powder accounts for the mass of the Fe powder30.02-2% of the total mass of Al alloy raw material powder, and the mass of the Zr powder accounts for the mass of the Fe30.08-5% of the total mass of the Al alloy raw material powder.
In one embodiment, in the FeAl alloy raw material powder, the mass ratio of the Fe powder to the Al powder is (2.2-4): 1, the mass of the amorphous B powder accounts for 0.02-2% of the total mass of the FeAl alloy raw material powder, and the Al powder2O3The mass of the particles accounts for 4-15% of the total mass of the FeAl alloy raw material powder.
In one embodiment, the FeAl alloy raw powder further comprises MoSi2Said MoSi2Accounting for 0.1 to 3 percent of the total mass of the FeAl alloy raw material powder.
In one embodiment, the Fe3In the Al alloy raw material powder, the mass of the amorphous B powder accounts for the Fe30.02-0.8% of the total mass of the Al alloy raw material powder; in the FeAl alloy raw material powder, the mass of the amorphous B powder accounts for 0.02-0.8% of the total mass of the FeAl alloy raw material powder; the Al is2O3The particle diameter of the particles is less than 10 μm.
In one embodiment, the laser cladding conditions are: the laser power is 1.5-3.5 kw, the scanning speed is 30-300 mm/s, and the spot diameter is 1-10 mm.
In one embodiment, the annealing temperature is 200 ℃ to 450 ℃.
In addition, the application also provides an application of the iron-aluminum alloy composite reinforced aluminum-based material in a high-speed rail transit brake disc.
The iron-aluminum alloy composite reinforced aluminum-based material is prepared by mixing FeAl phase, B phase and Al2O3FeAl alloy layer composed of Fe3Al phase and ZrB2Phase composition of Fe3Compared with FeAl with a B2 structure, the Al alloy layer has better room-temperature ductility and toughness and is closer to the thermal expansion coefficient of the aluminum-based alloy layer, and the Al alloy layer is positioned between the FeAl alloy layer and the aluminum-based alloy layer to play a role in stress buffering, so that the occurrence and the expansion of cracks under thermal stress in repeated and rapid braking are effectively prevented; compared with Fe3Al phase and ZrB2Phase composition of Fe3An Al alloy layer consisting of FeAl phase, B phase and Al2O3The FeAl alloy layer formed by the phase has higher specific strength and better corrosion resistance, and can effectively improve the wear resistance and the damage resistance when used as a surface layer.
In addition, the iron-aluminum intermetallic compound not only has excellent high-temperature oxidation resistance, sulfidation corrosion resistance and wear resistance, but also does not contain precious metals and is low in price. By metallurgy on the surface of aluminum-based alloysBound Fe3Al alloy layer, then Fe3The surface of the Al alloy layer is metallurgically bonded with the FeAl alloy layer, so that the aluminum alloy layer and the Fe are bonded3Between Al alloy layers and Fe3The bonding force between the Al alloy layer and the FeAl alloy layer is greatly improved, and the aluminum-iron alloy has the excellent corrosion resistance and wear resistance of the iron-aluminum intermetallic compound, and simultaneously retains the advantages of high thermal conductivity, light weight and the like of the aluminum-based alloy. The material is used for the brake disc of high-speed rail transit, so that the production cost can be greatly reduced, the service temperature of the brake disc can be remarkably improved, and the service life of the brake disc can be remarkably prolonged.
Drawings
FIG. 1 is the metallurgically bonded Fe prepared in example 13A gold phase diagram of the Al alloy layer and the Al alloy layer;
FIG. 2 is a graph showing the results of a friction test of the FeAl alloy layer prepared in example 1;
FIG. 3 is a graph showing the results of three repeated frictional wear tests performed on the FeAl alloy layer prepared in example 1;
FIG. 4 is a graph showing the results of a friction test of the FeAl alloy layer prepared in example 2;
FIG. 5 is a graph showing the results of three repeated frictional wear tests performed on the FeAl alloy layer prepared in example 2;
FIG. 6 is a graph showing the results of a friction test of the FeAl alloy layer prepared in example 3;
fig. 7 is a graph showing the results of three repeated frictional wear tests performed on the FeAl alloy layer prepared in example 3.
Detailed Description
In order that the invention may be more fully understood, a more particular description of the invention will now be rendered by reference to specific embodiments thereof that are illustrated in the appended drawings. This invention may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete.
Unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. The terminology used in the description of the invention herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention. As used herein, the term "and/or" includes any and all combinations of one or more of the associated listed items.
The preparation method of the iron-aluminum alloy composite reinforced aluminum-based composite material comprises the following steps of S110-S140:
s110, in a protective gas atmosphere, ball-milling and mixing Fe powder, Al powder, amorphous B powder and Zr powder in proportion to obtain Fe3Al alloy raw material powder.
In step S110, the mixing ratio of Fe powder and Al powder is controlled to produce Fe mainly having a DO3 structure3An Al phase. In addition, by adding proper amount of amorphous B powder and Zr powder, Zr reacts with B to generate ZrB2To improve Fe3The grain structure of the Al alloy avoids the occurrence of brittle fracture.
In this embodiment, Fe3In the Al alloy raw material powder, the mass ratio of Fe powder to Al powder is (4-7): 1, and the mass of amorphous B powder accounts for Fe30.02-2% of the total mass of Al alloy raw material powder, and the mass of Zr powder accounts for Fe30.08-5% of the total mass of the Al alloy raw material powder.
Further, the mass of the amorphous B powder is Fe30.02-0.8% of the total mass of the Al alloy raw material powder.
The Fe powder, the Al powder, the amorphous B powder and the Zr powder are ball-milled and mixed in proportion in a protective gas atmosphere, so that an oxide film can be prevented from being generated to influence the subsequent aluminum-based alloy layer and Fe3And (4) combining the Al alloy layers.
In this embodiment, the protective gas atmosphere in step S110 is an argon atmosphere or a helium atmosphere.
S120, in a protective gas atmosphere, mixing Fe powder, Al powder, amorphous B powder and Al powder2O3The particles are mixed according to a proportion to obtain FeAl alloy raw material powder.
In step S120, the mixing ratio of Fe powder and Al powder is controlled to mainly produce a FeAl phase having a B2 structure. In addition, the FeAl alloy is improved by adding proper amount of amorphous B powderPlasticity and toughness. By adding appropriate amount of Al2O3The particles are compounded with the FeAl phase, the FeAl phase and the FeAl phase have good surface wettability, and the FeAl phase can play a role in toughening and reinforcing by utilizing a dispersion strengthening mechanism and a fine grain strengthening mechanism. Namely Al2O3The particles exist in the crystal and outside the crystal, and under the pinning effect, the expansion of a large number of dislocations in the matrix phase can be effectively hindered, and the crack propagation path is increased, so that the fracture energy of the FeAl alloy layer is improved. Further, by adding an appropriate amount of Al2O3The particles can also be used to adjust and control the coefficient of friction so that the FeAl alloy layer has excellent wear resistance as a surface layer.
In the present embodiment, the mass ratio of Fe powder to Al powder in the FeAl alloy raw material powder is (2.2-4): 1, the mass of amorphous B powder is 0.02-2% of the total mass of the FeAl alloy raw material powder, and Al powder2O3The mass of the particles accounts for 4-15% of the total mass of the FeAl alloy raw material powder.
Further, the mass of the amorphous B powder accounts for 0.02-0.8% of the total mass of the FeAl alloy raw material powder.
Further, Al2O3The particle size of the particles needs to be controlled below 10 mu m so as to maximize the toughening and reinforcing effects and the wear resistance and damage resistance of the particles. Further, Al2O3The particle size of the particles is 10 nm-10 mu m.
In other embodiments, the FeAl alloy raw powder may further include MoSi if it is desired to reduce the friction coefficient2. By adding appropriate amount of MoSi2As a lubricating component, the friction coefficient of the FeAl alloy layer is adjusted to meet the specified requirement.
Further, MoSi2Accounting for 0.1 to 3 percent of the total mass of the FeAl alloy raw material powder. It is understood that the FeAl alloy raw powder herein is a powder including MoSi2The raw powder of FeAl alloy.
Further, the protective gas atmosphere in step S120 is an argon atmosphere or a helium atmosphere.
S130, mixing the Fe3Al alloy raw material powder is laid on the surface of the aluminum-based alloy, and is annealed after laser cladding in protective gas atmosphere to obtainTo metallurgically bound Fe3An Al alloy layer and an aluminum-based alloy layer.
In the present embodiment, the aluminum-based alloy is an Al-Fe-V-Si aluminum alloy in which the mass fraction of Fe is 8.5%, the mass fraction of V is 1.3%, the mass fraction of Si is 1.9%, and the balance is aluminum.
It should be noted that the aluminum-based alloy can be selected according to specific use requirements and Fe3An Al-based alloy whose thermophysical properties are matched with those of the Al alloy is not limited to the Al-Fe-V-Si aluminum alloy described above.
By laser cladding Fe on the surface of aluminum-based alloy3Al alloy layer made of Fe3The higher content of iron in the Al alloy raw powder can effectively dilute the aluminum in the aluminum-based alloy, thereby avoiding FeAl2、Fe2Al5、FeAl3The generation of an iso-brittle phase, while mainly generating Fe with higher ductility and toughness3An Al phase. At the same time, by Fe3ZrB generated by reaction of amorphous B powder and Zr powder in Al alloy raw powder2Phase, effective in improving Fe3The grain structure of the Al alloy avoids brittle fracture and prevents pores and cracks. In addition, due to Fe3The Al alloy layer and the aluminum alloy layer are metallurgically bonded by adopting a laser cladding technology, so that Fe can be effectively improved3Bonding strength of Al alloy layer and Al alloy layer, and Fe3The Al alloy layer has a thermal expansion coefficient close to that of the Al alloy layer, and the Al alloy layer has excellent heat conductivity, so that Fe3The thermal stress generated by the Al alloy layer under the preparation working condition is very small and can be almost ignored.
In this embodiment, the protective gas atmosphere is an argon atmosphere or a helium atmosphere, a fiber laser is used for laser cladding, and the laser cladding conditions are as follows: the laser power is 1.5-3.5 kw, the scanning speed is 30-300 mm/s, and the spot diameter is 1-10 mm.
In the present embodiment, the annealing temperature is 200 to 450 ℃.
It is understood that Fe3There may be a very small amount of other intermetallic Fe-Al compounds at the interface between Al alloy layer and Al alloy layer, but because of Fe3Al alloyThe higher content of iron powder in the gold raw powder has the dilution effect, and the Fe with higher plasticity and toughness is mainly generated3An Al phase.
S140, laying the FeAl alloy raw material powder on Fe3And (3) carrying out laser cladding on the surface of the Al alloy layer in a protective gas atmosphere and then annealing to obtain the iron-aluminum alloy composite reinforced aluminum-based material.
In this embodiment, the protective gas atmosphere is an argon atmosphere or a helium atmosphere, the laser cladding employs a fiber laser, and the laser cladding conditions are as follows: the laser power is 1.5-3.5 kw, the scanning speed is 30-300 mm/s, and the spot diameter is 1-10 mm.
In the present embodiment, the annealing temperature is 200 to 450 ℃.
Composed of FeAl phase, B phase and Al2O3The FeAl alloy layer formed by the phase has higher specific strength and better corrosion resistance, and can effectively improve the wear resistance and the damage resistance when used as a surface layer.
The iron-aluminum alloy composite reinforced aluminum-based material utilizes a laser cladding technology to enable an aluminum-based alloy layer and Fe to be3Between Al alloy layers and Fe3Fe with greatly improved binding force between Al alloy layer and FeAl alloy layer and better plasticity3The Al alloy layer is used as the intermediate layer, can play a role in stress buffering, can effectively prevent the occurrence and the expansion of cracks under thermal stress in repeated and rapid braking, the Al alloy layer is used as the substrate layer, can play a good role in heat conduction, and the high-hardness and wear-resistant FeAl alloy layer is used as the surface layer, can play a role in wear resistance and corrosion resistance, and is used for a high-speed rail transit brake disc, so that the production cost can be greatly reduced, the service temperature of the brake disc can be remarkably improved, and the service life of the brake disc can be.
In addition, the order of steps S110 and S120 is not limited, and Fe may be prepared first3The Al alloy raw material powder may be prepared first or simultaneously, as long as the corresponding raw material powder is prepared before the corresponding layer is prepared.
The following are specific examples.
Example 1
(1) In an argon atmosphere, 850g of Fe powder, 150g of Al powder, 8g of amorphous B powder and 1g of Zr powder were ball-milled and mixed to obtain Fe3Al alloy raw material powder.
(2) In an argon atmosphere, 750g of Fe powder, 250g of Al powder, 10g of amorphous B powder and 100g of Al powder2O3And ball-milling and mixing the particles to obtain FeAl alloy raw material powder.
(3) Mixing the above Fe3Laying Al alloy raw material powder on the surface of Al-Fe-V-Si aluminum alloy, carrying out laser cladding in the argon protective atmosphere, and then annealing for 2 hours at 450 ℃ to obtain metallurgically bonded Fe3An Al alloy layer and an aluminum-based alloy layer. Wherein, the laser cladding conditions are as follows: the laser power is 3kw, the scanning speed is 300mm/s, and the spot diameter is 3 mm.
(4) Laying the FeAl alloy raw material powder on Fe3And (3) carrying out laser cladding on the surface of the Al alloy layer in the argon protective atmosphere, and then annealing at 200 ℃ to obtain the iron-aluminum alloy composite reinforced aluminum-based material. Wherein, the laser cladding conditions are as follows: the laser power is 3.5kw, the scanning speed is 300mm/s, and the spot diameter is 3 mm.
Metallurgically bonded Fe prepared in example 13The gold phase diagram of the Al alloy layer and the aluminum-based alloy layer is shown in fig. 1. From FIG. 1, it can be seen that the Al-based alloy layer and Fe3The Al alloy layer has good interface bonding.
The hardness of the FeAl alloy layer sample prepared in example 1 was measured to be around 3.5 GPa.
Three repeated frictional wear tests were performed on the FeAl alloy layer samples prepared in example 1 under the following experimental conditions: the pair of SiC pieces was rubbed at a speed of 1m/s for 1000m under a pressure of 23N, and as a result, as shown in FIG. 2, it was found from FIG. 2 that the FeAl alloy layer had an average friction coefficient of 0.78.
Three repeated frictional wear tests were performed on the FeAl alloy layer samples prepared in example 1 under the following experimental conditions: the result of rubbing 1000m with SiC at a rubbing speed of 1m/s under a pressure of 23N was as shown in FIG. 3, and it was found from FIG. 3 that the average wear amount of the FeAl alloy layer was 8.3 mg.
Example 2
(1) In the argon atmosphere, the reaction kettle is filled with nitrogen,850g of Fe powder, 150g of Al powder, 12g of amorphous B powder and 10g of Zr powder were mixed by ball milling to obtain Fe3Al alloy raw material powder.
(2) 700g of Fe powder, 300g of Al powder, 15g of amorphous B powder and 50g of Al powder were mixed under an argon atmosphere2O3And ball-milling and mixing the particles to obtain FeAl alloy raw material powder.
(3) Mixing the above Fe3Laying Al alloy raw material powder on the surface of Al-Fe-V-Si aluminum alloy, annealing for 3 hours at 300 ℃ after laser cladding to obtain metallurgically bonded Fe3An Al alloy layer and an aluminum-based alloy layer. Wherein, the laser cladding conditions are as follows: the laser power is 3kw, the scanning speed is 250mm/s, and the spot diameter is 3 mm.
(4) Laying the FeAl alloy raw material powder on Fe3And (3) annealing at 300 ℃ after laser cladding is carried out on the surface of the Al alloy layer to obtain the iron-aluminum alloy composite reinforced aluminum-based material. Wherein, the laser cladding conditions are as follows: the laser power is 2.5kw, the scanning speed is 300mm/s, and the spot diameter is 3 mm.
The hardness test of the FeAl alloy layer sample prepared in the example 2 is about 3.3 GPa.
The FeAl alloy layer sample prepared in example 2 was subjected to three repeated frictional wear tests under the following experimental conditions: the result of rubbing with SiC at a couple of 1000m under a pressure of 23N at a rubbing speed of 1m/s is shown in FIG. 4, and it can be seen from FIG. 4 that the FeAl alloy layer had an average friction coefficient of 0.70.
The FeAl alloy layer sample prepared in example 2 was subjected to three repeated frictional wear tests under the following experimental conditions: the result of rubbing 1000m with SiC at a rubbing speed of 1m/s under a pressure of 23N was as shown in FIG. 5, and it was found from FIG. 5 that the average wear amount of the FeAl alloy layer was 9.3 mg.
Example 3
(1) In an argon atmosphere, 800g of Fe powder, 200g of Al powder, 10g of amorphous B powder and 5g of Zr powder were ball-milled and mixed to obtain Fe3Al alloy raw material powder.
(2) 700g of Fe powder, 300g of Al powder, 15g of amorphous B powder, 50g of MoSi2 powder and 20g of MoSi2 powder are mixed by ball milling in an argon atmosphere to obtain FeAl alloy raw material powder.
(3) Mixing the aboveFe3Laying Al alloy raw material powder on the surface of Al-Fe-V-Si aluminum alloy, annealing for 4 hours at 200 ℃ after laser cladding to obtain metallurgically bonded Fe3An Al alloy layer and an aluminum-based alloy layer. Wherein, the laser cladding conditions are as follows: the laser power is 3.5kw, the scanning speed is 300mm/s, and the spot diameter is 3 mm.
(4) Laying the FeAl alloy raw material powder on Fe3And (3) annealing at 450 ℃ after laser cladding is carried out on the surface of the Al alloy layer to obtain the iron-aluminum alloy composite reinforced aluminum-based material. Wherein, the laser cladding conditions are as follows: the laser power is 2.5kw, the scanning speed is 300mm/s, and the spot diameter is 3 mm.
The hardness of the FeAl alloy layer sample prepared in the example 3 is about 3.2 GPa.
Three repeated friction and wear tests were performed on the FeAl alloy layer sample prepared in example 3 under the following experimental conditions: the result of the double friction with SiC at a friction speed of 1m/s of 1000m under a pressure of 23N is shown in FIG. 6, and it can be seen from FIG. 6 that the average friction coefficient of the FeAl alloy layer after lubrication with the addition of MoSi2 is 0.53.
Three repeated friction and wear tests were performed on the FeAl alloy layer sample prepared in example 3 under the following experimental conditions: the result of rubbing 1000m with SiC at a rubbing speed of 1m/s under a pressure of 23N was as shown in FIG. 7, and it was found from FIG. 7 that the average wear amount of the FeAl alloy layer was 6.8 mg.
Comparative example 1
Comparative example 1 is basically the same as example 1, except that comparative example 1 is obtained by laser cladding of a FeAl alloy layer on the surface of an Al-Fe-V-Si aluminum alloy and then laser cladding of Fe on the surface of the FeAl alloy layer3Al alloy layer, and as a result, Fe was found3The wear resistance of the Al alloy layer is significantly lower than that of the FeAl alloy layer, and under thermal fatigue and stress fatigue of repeated braking, crack propagation between the FeAl layer and the aluminum alloy layer is easily caused by brittleness of the FeAl alloy layer, which in turn causes peeling and breakage at the interface.
Comparative example 2
Comparative example 2 is substantially the same as example 1 except that Fe is present in comparative example 23The Fe powder in the Al alloy raw material powder is 950g, AThe powder amount was 50g, and it was found that Fe having a DO3 structure could not be formed at all3The Al intermetallic compound layer exists in a form in which Al atoms are solid-dissolved in the ferrite.
Comparative example 3
Comparative example 3 is substantially the same as example 1 except that the raw powder of FeAl alloy in comparative example 3 contains 650g of Fe powder and 350g of Al powder. As a result, it was found that too high Al content makes the brittleness of FeAl more remarkable, thereby affecting the stability during friction, and even though B and Zr are added to achieve toughening and strengthening, the room temperature plasticity of FeAl is improved only slightly.
Comparative example 4
Comparative example 4 is substantially the same as example 1 except that Fe is present in comparative example 43Amorphous B powder and/or Zr powder are not added in the Al alloy raw material powder. As a result, it was found that Fe was reduced without adding amorphous B powder and/or Zr powder3Ductility and toughness of Al material, easily leading to Fe3Hydrogen embrittlement and reduction in ductility and toughness of the Al layer.
Comparative example 5
Comparative example 5 is substantially the same as example 1 except that Fe is present in comparative example 53Amorphous B powder and/or Al are not added in Al alloy raw material powder2O3And (3) granules. As a result, it was found that the amorphous B powder and/or Al were not added2O3The particles will reduce Fe3Ductility and toughness of Al material, easily leading to Fe3Hydrogen embrittlement and reduction in ductility and toughness of the Al layer.
The above-mentioned embodiments only express several embodiments of the present invention, and the description thereof is more specific and detailed, but not construed as limiting the scope of the present invention. It should be noted that, for a person skilled in the art, several variations and modifications can be made without departing from the inventive concept, which falls within the scope of the present invention. Therefore, the protection scope of the present patent shall be subject to the appended claims.
Claims (10)
1. The iron-aluminum alloy composite reinforced aluminum-based material is characterized by comprising an aluminum alloyGold layer, Fe metallurgically bonded to said aluminium-based alloy layer3Al alloy layer and Fe3A FeAl alloy layer metallurgically bonded with the Al alloy layer, the Fe3The Al alloy layer is mainly made of Fe3Al phase and ZrB2The FeAl alloy layer mainly consists of a FeAl phase, a B phase and Al2O3Phase composition.
2. The iron-aluminum alloy composite reinforced aluminum-based material of claim 1, wherein the FeAl alloy layer further comprises MoSi2And (4) phase(s).
3. The method for preparing the iron-aluminum alloy composite reinforced aluminum-based material of claim 1 or 2, which comprises the following steps:
in protective gas atmosphere, ball milling and mixing Fe powder, Al powder, amorphous B powder and Zr powder according to proportion to obtain Fe3Al alloy raw material powder;
in protective gas atmosphere, Fe powder, Al powder, amorphous B powder and Al powder2O3Mixing the particles in proportion to obtain FeAl alloy raw material powder;
subjecting said Fe to3Al alloy raw material powder is laid on the surface of the aluminum-based alloy, and is annealed after laser cladding in protective gas atmosphere to obtain metallurgically bonded Fe3An Al alloy layer and an Al alloy layer;
laying the FeAl alloy raw material powder on the Fe3And carrying out laser cladding on the surface of the Al alloy layer in a protective gas atmosphere and then annealing to obtain the iron-aluminum alloy composite reinforced aluminum-based material.
4. The method as claimed in claim 3, wherein the Fe-Al alloy is Fe3In the Al alloy raw material powder, the mass ratio of the Fe powder to the Al powder is (4-7): 1, and the mass of the amorphous B powder accounts for the mass of the Fe powder30.02-2% of the total mass of Al alloy raw material powder, and the mass of the Zr powder accounts for the mass of the Fe30.08-5% of the total mass of the Al alloy raw material powder.
5. The method for preparing an iron-aluminum alloy composite reinforced aluminum-based material as claimed in claim 3, wherein the FeAl alloy raw powder has a mass ratio of Fe powder to Al powder of (2.2-4): 1, the amorphous B powder accounts for 0.02-2% of the total mass of the FeAl alloy raw powder, and the Al powder accounts for the total mass of the FeAl alloy raw powder2O3The mass of the particles accounts for 4-15% of the total mass of the FeAl alloy raw material powder.
6. The method as claimed in claim 3, wherein the raw FeAl alloy powder further comprises MoSi2Said MoSi2Accounting for 0.1 to 3 percent of the total mass of the FeAl alloy raw material powder.
7. The method for preparing the iron-aluminum alloy composite reinforced aluminum-based material as claimed in any one of claims 3 to 6, wherein the Fe is Fe3In the Al alloy raw material powder, the mass of the amorphous B powder accounts for the Fe30.02-0.8% of the total mass of the Al alloy raw material powder; in the FeAl alloy raw material powder, the mass of the amorphous B powder accounts for 0.02-0.8% of the total mass of the FeAl alloy raw material powder; the Al is2O3The particle diameter of the particles is less than 10 μm.
8. The method for preparing the iron-aluminum alloy composite reinforced aluminum-based material as claimed in claim 3, wherein the laser cladding conditions are as follows: the laser power is 1.5-3.5 kw, the scanning speed is 30-300 mm/s, and the spot diameter is 1-10 mm.
9. The method as claimed in claim 3, wherein the annealing temperature is 200-450 ℃.
10. Use of the iron aluminum alloy composite reinforced aluminum-based material of claim 1 or 2 in a brake disc for high-speed rail transit.
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| PCT/CN2022/073121 WO2022111739A1 (en) | 2020-11-30 | 2022-01-21 | Iron-aluminum alloy composite reinforced aluminum-based material, preparation method therefor and application thereof |
| ZA2023/04599A ZA202304599B (en) | 2020-11-30 | 2023-04-20 | Iron-aluminum alloy composite-reinforced aluminum-based material, and preparation method and use thereof |
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| CN115354319B (en) * | 2022-08-29 | 2023-12-08 | 江苏徐工工程机械研究院有限公司 | High-hardness corrosion-resistant coating structure for surface of large-sized cylinder part and preparation method thereof |
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