CN114875278A - Ti-Al series gradient composite material and preparation method thereof - Google Patents
Ti-Al series gradient composite material and preparation method thereof Download PDFInfo
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- CN114875278A CN114875278A CN202210570508.XA CN202210570508A CN114875278A CN 114875278 A CN114875278 A CN 114875278A CN 202210570508 A CN202210570508 A CN 202210570508A CN 114875278 A CN114875278 A CN 114875278A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
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- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D13/00—Centrifugal casting; Casting by using centrifugal force
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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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
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- 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
Abstract
The invention provides a Ti-Al gradient composite material and a preparation method thereof. The Ti-Al gradient composite material comprises an inner layer and an outer layer surrounding the inner layer, wherein the inner layer is made of aluminum alloy, and the outer layer comprises TiAl 3 Intermetallic compound and dispersed in TiAl 3 Polytype TiC particles in the intermetallic compound, the polytype TiC particles comprise B doped TiC particles formed by B atoms occupying C vacancies in TiC crystals and TiC particles not doped with B atoms. The Ti-Al series gradient composite material has improved strength and toughness.
Description
Technical Field
The invention relates to the field of metal materials, in particular to a Ti-Al gradient composite material and a preparation method thereof.
Background
Having a plurality of intermetallic compounds in the Ti-Al alloy, e.g. TiAl 3 And TiAl and the like. The creep resistance and the oxidation resistance of the intermetallic compound are superior to those of titanium, but the intermetallic compound has large room temperature brittleness and lower medium-high temperature strength, and the two main short plates severely limit the application of the Ti-Al intermetallic compound.
Therefore, how to improve the toughness and the strength of the Ti-Al intermetallic compound is a problem which needs to be solved for expanding the application of the Ti-Al alloy.
Disclosure of Invention
The invention aims to provide a Ti-Al gradient composite material with improved toughness and strength and a preparation method thereof.
According to an aspect of the present invention, there is provided a Ti-Al-based gradient composite material including an inner layer and an outer layer surrounding the inner layer, the inner layer being an aluminum alloy, the outer layer including TiAl 3 Intermetallic compound and dispersed in TiAl 3 Polytype TiC particles in the intermetallic compound, the polytype TiC particles comprise B doped TiC particles formed by B atoms occupying C vacancies in TiC crystals and TiC particles not doped with B atoms.
Optionally, the amount of B doped in the B-doped TiC particles is 0.1 wt% to 10 wt%.
Optionally, based on 100 wt% of the Ti-Al gradient composite material, the mass percentage of the C element is 0.1 wt% to 0.8 wt%, the mass percentage of the B element is 0.01 wt% to 0.08 wt%, the mass percentage of the Ti element is 2 wt% to 12 wt%, and the balance is Al, wherein the content of the polytype TiC particles is 0.5 wt% to 4 wt%.
Optionally, the polytype TiC particles are generated in situ and are dispersed and distributed in the TiAl of the outer layer 3 MetalAn intermediate compound matrix.
Optionally, the polytype TiC particles have dual-scale features of nanometer scale and micrometer scale, and the size of the polytype TiC particles is between 20nm and 1.5 μm.
Optionally, the inner layer comprises an Al matrix, the TiAl in the outer layer 3 Intermetallic compounds and the multi-type TiC particles are also contained in the Al matrix of the inner layer.
According to another aspect of the present invention, there is provided a method for manufacturing a Ti — Al-based gradient composite material, the method comprising: preparing raw materials, namely an Al source, a Ti source, an Al-C alloy and an Al-B alloy, and dividing the Ti source into two parts, wherein the Al-C alloy contains Al 4 C 3 The Al-B alloy includes AlB 2 (ii) a Adding an Al source into a smelting furnace, heating and melting to 850-950 ℃, and adding a first part of Ti source into the melt; after the first part of Ti source is completely dissolved, heating the alloy melt to 900-1100 ℃, adding Al-C alloy and Al-B alloy, and standing for reaction for 5-45 min; adding a second portion of the Ti source to the alloy melt and dissolving the second portion of the Ti source; and pouring the alloy melt into a centrifugal casting machine to obtain the Ti-Al gradient composite material.
Optionally, the step of pouring the alloy melt into a centrifugal casting machine to obtain the Ti-Al gradient composite material comprises: cooling the alloy melt to 750-850 ℃, and then heating to 950-1050 ℃; and cooling the alloy melt to 780-820 ℃, pouring the alloy melt into a centrifugal casting machine for separation, solidification and molding to obtain the Ti-Al gradient composite material.
Optionally, the Al source is pure aluminum, the Ti source is Ti particles, the Al-C alloy is an Al-2C alloy, the Al-B alloy is an Al-3B alloy, and the weight ratio of C is 2 wt% based on the total weight of the Al-2C alloy and the weight ratio of B is 3 wt% based on the Al-3B alloy. The raw materials were prepared according to the following ingredients contents: based on 100 wt% of the Ti-Al series gradient composite material, the mass percent of the C element is 0.1-0.8 wt%, the mass percent of the B element is 0.01-0.08 wt%, the mass percent of the Ti element is 2-12 wt%, and the balance is Al.
Optionally, after adding the first portion of Ti source to the melt, the mass ratio of Ti element to C element in the melt is 4: 1.
According to the Ti-Al gradient composite material, the inner layer is made of aluminum alloy, the specific gravity is small, and the outer layer is made of polytype TiC reinforced TiAl 3 Intermetallic compound based composite material, thereby realizing TiAl 3 The toughening and the reinforcement of the Ti-Al series gradient composite material ensure that the Ti-Al series gradient composite material has comprehensive mechanical properties of low specific gravity, high strength and high toughness.
According to the manufacturing method of the Ti-Al gradient composite material provided by the embodiment of the invention, the adopted raw materials are low in price, low in cost, high in efficiency, simple and convenient to operate, simple in equipment, green, environment-friendly and pollution-free, and strong in operability, and the prepared Ti-Al gradient composite material is stable in product quality, high in material utilization rate and high in industrialization potential.
Drawings
The above and other objects, features and advantages of the present invention will become more apparent from the following detailed description when taken in conjunction with the accompanying drawings in which:
FIG. 1 is a microstructure of a Ti-Al based gradient composite according to an embodiment of the present invention;
FIG. 2 is an electron probe composition analysis of the Ti-Al based gradient composite material shown in FIG. 1.
Detailed Description
Hereinafter, embodiments of the present invention will be described. This invention may, however, be embodied in many different forms and should not be construed as limited to the specific embodiments set forth herein. Rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the scope of the invention to those skilled in the art.
It will be understood that when the terms "comprises" and/or "comprising" are used in this specification, they specify the presence of stated materials and/or ingredients, but do not preclude the presence or addition of one or more other materials and/or ingredients.
Gradient composite material of Ti-Al series
Fig. 1 is a microstructure of a Ti-Al based gradient composite material according to an embodiment of the present invention, and fig. 2 is an electron probe composition analysis of the Ti-Al based gradient composite material shown in fig. 1. Hereinafter, a Ti — Al-based gradient composite material according to an embodiment of the present invention will be described with reference to fig. 1 and 2.
As shown in FIGS. 1 and 2, a Ti-Al based gradient composite according to an embodiment of the present invention may include an inner layer 10 and an outer layer 20 surrounding the inner layer 10, the inner layer 10 being an aluminum alloy, the outer layer 20 including TiAl 3 Intermetallic compound and dispersed in TiAl 3 Polytype TiC particles in intermetallic compounds.
According to embodiments of the present invention, the outer layer 20 may surround at least a portion of the inner layer 10, and is not limited to completely surrounding the inner layer 10. Fig. 1 is an image obtained by scanning a cross section of a Ti — Al-based gradient composite material using a scanning electron microscope, and thus in fig. 1, an inner layer 10 is disposed below and an outer layer 20 is disposed on the inner layer 10.
In the outer layer 20, TiAl according to an embodiment of the present invention 3 The intermetallic compound can form a substrate of the outer layer, and the multi-type TiC particles can be dispersed and distributed in TiAl 3 An intermetallic compound matrix.
According to an embodiment of the present invention, the polytype TiC particles may include B-doped TiC particles formed by B atoms occupying C vacancies in TiC crystals and TiC particles not doped with B atoms. The number ratio of the B-doped TiC particles to the TiC particles not doped with B atoms is not particularly limited.
According to the embodiment of the invention, the crystal structure of the B doped TiC particles is consistent with that of TiC, and the B doping amount in the B doped TiC particles can be 0.1 wt% -10 wt%. By doping trace B element, the structural stability and the thermal stability of TiC particles can be improved, and the stability with TiAl can be improved 3 The interface matching degree of the substrate.
According to the embodiment of the invention, based on 100 wt% of the Ti-Al series gradient composite material, the mass percent of the C element is 0.1-0.8 wt%, the mass percent of the B element is 0.01-0.08 wt%, the mass percent of the Ti element is 2-12 wt%, and the balance is Al. According to an embodiment of the present invention, the amount of the multi-type TiC particles is preferably 0.5 wt% to 4 wt% based on 100 wt% of the Ti — Al based gradient composite material. When the content of the polytype TiC particles is less than 0.5 wt% or exceeds 4 wt%, the reinforcing effect on the Ti-Al series gradient composite material may be less obvious.
According to the embodiment of the invention, the multi-type TiC particles are generated in situ and are dispersed and distributed in the TiAl of the outer layer 20 3 An intermetallic compound matrix.
Some documents in the prior art report the reinforcement of Ti-Al composites by the addition of TiC particles. For example, the literature (university of Jinan Master academic thesis, official derivatives, 2003) prepares TiAl composites reinforced with added TiC using SPS sintering technology. The document (J.Mater.Eng.Perform.26(2017) 3457-3464) also prepares additional TiC-reinforced TiAl composites using SPS. Literature (Optics)&Laser Technology 112(2019)339-348) mixing Ti powder, Al powder and TiC powder, and preparing the TiC-reinforced TiAl-based composite material through Laser cladding, wherein the TiC is abnormally large in size and grows in a dendritic mode particularly when the size reaches a micrometer. The literature (Materials and technology 43(2009) 239- 3 The composite material has low density, and when the content of TiC is more than 10 vol%, 5-10% of free Al and 5% of free Ti are required to be added to ensure the density of the material.
According to the embodiment of the invention, because the polytype TiC particles are generated through in-situ reaction, the polytype TiC particles and TiAl are arranged between the polytype TiC particles 3 The intermetallic compound has good wettability and firm interface combination, is beneficial to fully exerting the load transfer between the matrix and the reinforced phase, and has higher strength, modulus and other properties compared with the added particles.
According to an embodiment of the invention, as shown in figure 1, polytype TiC particles have dual-scale features of nano-scale and micro-scale, and the size of the polytype TiC particles can be between 20nm and 1.5 μm.
According to an embodiment of the present invention, as shown in FIG. 1, the inner layer 10 comprises an Al matrix and the TiAl in the outer layer 20 3 Intermetallic compounds and multi-type TiC particles may also be included in a small amountContained in the Al matrix of the inner layer 10. This is because the Ti — Al system gradient composite material according to the embodiment of the present invention may be formed by a molding manner of centrifugal casting. Some polytype TiC particles will remain in the Al matrix of the inner layer 10, subject to factors such as the forming process, melt viscosity, particle size, etc. Meanwhile, a small part of Ti can be dissolved in the aluminum melt, and TiAl is used in the process of cooling 3 Intermetallic compounds precipitate out and eventually remain in the Al matrix of the inner layer 10 due to excessive melt viscosity.
According to the Ti-Al gradient composite material, the inner layer is made of aluminum alloy, the specific gravity is small, and the outer layer is made of polytype TiC reinforced TiAl 3 Intermetallic compound based composite material, thereby realizing TiAl 3 The toughening and the reinforcement of the Ti-Al series gradient composite material ensure that the Ti-Al series gradient composite material has comprehensive mechanical properties of low specific gravity, high strength and high toughness. Hereinafter, the toughening and reinforcing mechanism will be described in detail.
First, the Ti — Al-based gradient composite material according to the present invention has improved toughness. Specifically, the polytype TiC particles can effectively improve TiAl 3 Toughness of the intermetallic matrix. Polytype TiC and TiAl 3 The chemical compatibility and the mechanical compatibility are good, and the polytype TiC can increase the crack propagation path and the crack propagation resistance in the load transfer process, generate the crack deflection effect and effectively improve TiAl 3 Brittleness of intermetallic compounds. In addition, polytype TiC and TiAl 3 The thermal stress between two phases makes the polytype TiC be stressed, because the compression resistance of polytype TiC ceramic is greatly superior to that of tensile resistance, and TiAl 3 The intermetallic compound has small elastic modulus, can effectively absorb deformation energy after being stressed, and the generated thermal mismatch effect can effectively improve TiAl 3 Brittleness of intermetallic compounds. Therefore, the Ti-Al based gradient composite material according to the present invention has improved toughness.
In addition, the Ti-Al based gradient composite material according to the present invention has improved strength. Specifically, the polytype TiC particles can effectively improve TiAl 3 Strength of the intermetallic matrix. When the material is loaded, partial load can be transferred from the matrix to the multi-type TiC particles of the strengthening phase through interfacial shear force, so that the stronger strengthening phaseThe good interface combination brought by the polytype TiC particles generated in situ can play a role in further contributing to playing a role in strengthening load transfer. Meanwhile, because of polytype TiC and TiAl 3 The difference of the thermal expansion coefficients of the two phases causes thermal dislocation around the reinforced phase, and due to the blocking effect and pinning effect of the polytype TiC on the dislocation movement, the dislocations and the dislocations generated in the subsequent processing process are retained, so that a remarkable dislocation strengthening effect is generated. In addition, in the bearing process, the polytype TiC can also play an Orowan strengthening mechanism, and in the process, dislocation movement needs to overcome not only the blocking effect of a nanometer precipitated phase, but also the reaction force given by a dislocation loop. In conclusion, the polytype TiC can strengthen TiAl due to the strengthening effect 3 Strength of the intermetallic compound. Therefore, the Ti — Al based gradient composite material according to the present invention has improved strength.
Preparation method of Ti-Al series gradient composite material
The invention provides a preparation method of a Ti-Al gradient composite material for in-situ synthesis of polytype TiC.
For the in-situ synthesis method, the literature (aeronautics report, 15, 1994) adopts Ti, Al and C powder as raw materials, and utilizes XD (thermal explosion) process to synthesize TiAl alloy and TiC/TiAl composite material, which shows that the exothermic reaction between Ti and Al can promote the synthesis of TiC, and the phase composition of the TiC/TiAl composite material is TiC + TiAl + Ti 3 And Al. However, the powder metallurgy process is subject to many limitations and is poor in safety. The Chinese patent with the publication number of CN111763939A discloses the preparation of nano-sized and micro-sized Ti and C powder and nanocrystalline TiAl 3 The powder is mixed and ball-milled to obtain TiAl 3 a/Ti/C composite powder; then TiAl is added 3 the/Ti/C composite powder is sprayed on the surface of a substrate by a cold spraying technology to obtain TiAl 3 a/Ti/C composite coating; finally, carrying out heat treatment on the coating to obtain multi-scale TiC ceramic phase reinforced TiAl 3 A TiAl two-phase composite coating. However, the manner of preparation of the composite coating is not suitable for bulk materials.
In order to overcome the limitation of the existing in-situ synthesis method, the invention provides a preparation method of a Ti-Al gradient composite material for in-situ synthesis of polytype TiC. The interface bonding of the reinforcing phase prepared by the in-situ method and the matrix is stronger, the distribution of the reinforcing phase is dispersed, and the size is controllable.
The method for manufacturing the Ti-Al gradient composite material according to the embodiment of the invention comprises the following steps: preparing raw materials including an Al source, a Ti source, an Al-C alloy and an Al-B alloy, and dividing the Ti source into two parts, wherein the Al-C alloy contains Al 4 C 3 The Al-B alloy includes AlB 2 (ii) a Adding an Al source into a smelting furnace, heating and melting to 850-950 ℃, and adding a first part of Ti source into the melt; after the first part of Ti source is completely dissolved, heating the alloy melt to 900-1100 ℃, adding Al-C alloy and Al-B alloy, and standing for reaction for 5-45 min; adding a second portion of the Ti source to the alloy melt and dissolving the second portion of the Ti source; and pouring the alloy melt into a centrifugal casting machine to obtain the Ti-Al gradient composite material.
First, the following raw materials may be prepared: an Al source, a Ti source, an Al-C alloy, and an Al-B alloy. Wherein the Al-C alloy contains Al 4 C 3 The Al-B alloy includes AlB 2 。
As an example, the Al source may be pure aluminum and the Ti source may be Ti particles. As an example, the Al-C alloy may be an Al-2C alloy with a weight ratio of C of 2 wt% based on the total weight of the Al-2C alloy. As an example, the Al-B alloy may be an Al-3B alloy, with the weight ratio of B being 3 wt% based on the Al-3B alloy.
According to an embodiment of the present invention, the above raw materials may be prepared in the following contents of components: based on 100 wt% of Ti-Al series gradient composite material, the mass percent of C element is 0.1-0.8 wt%, the mass percent of B element is 0.01-0.08 wt%, the mass percent of Ti element is 2-12 wt%, and the balance is Al.
According to an embodiment of the present invention, after the raw materials are prepared, pure aluminum may be first added to the melting furnace, heated to melt to 850 ℃ to 950 ℃, and a first portion of Ti source (e.g., Ti particles) is added to the melt. If the temperature is below 850 c, the titanium source may dissolve insufficiently or too slowly, and if the temperature exceeds 950 c, it may result in a waste of energy.
After the first part of Ti source is completely dissolved, heating the alloy melt to 900-1100 ℃, adding Al-C alloy (for example, Al-2C alloy) and Al-B alloy (for example, Al-3B alloy), and standing for reaction for 5-45 min.
Preferably, after the Al-2C alloy and the Al-3B alloy are added, the mass ratio of the Ti element to the C element in the melt is ensured to be basically 4:1, so that basically no redundant Ti or redundant C exists in the melt, and the in-situ reaction can be fully performed. If the Ti is excessive, the excessive dissolved Ti in the melt can be caused, and the synthesized TiC particles have too many hollow sites and are unstable; if C is excessive, it may result in excessive Al in the melt 4 C 3 And (4) phase(s).
According to an embodiment of the invention, an Al-2C alloy (wherein C is Al) is added 4 C 3 Form) and Al-3B alloy, the Ti in the melt will react with Al 4 C 3 In-situ reaction is carried out to generate TiC particles, and meanwhile, B element introduced by adding Al-3B alloy participates in the reaction process to dope the TiC particle vacancies, namely the doping of the in-situ reaction vacancies is carried out synchronously.
In the step of adding the Al-2C alloy and the Al-3B alloy, after the first part of Ti source is completely dissolved, the temperature is increased to 900-1100 ℃, and then the Al-2C alloy and the Al-3B alloy are added to ensure that Ti and Al can be mixed 4 C 3 The temperature at which the in situ reaction occurs and the temperature at which the B vacancies are doped. When the temperature is lower than 900 ℃, Ti and Al 4 C 3 Reaction may not occur or be insufficient, and the amount of B dissolved is low and vacancy doping is insufficient; when the temperature is higher than 1100 ℃, energy waste or melt sputtering may result.
The heat preservation time after the Al-2C alloy and the Al-3B alloy seed crystal alloy are added is 5min to 45min so as to ensure the sufficient reaction time. When the heat preservation time is less than 5min, the in-situ reaction and vacancy doping are insufficient, and when the heat preservation time is more than 45min, energy waste can be caused.
After the reaction is completed, a second portion of the Ti source is added to the alloy melt and dissolved. According to the embodiment of the invention, by adding the titanium source in two times, the first addition can effectively ensure the reaction with Al 4 C 3 In-situ reaction of particles and vacancy doping of B; adding for the second timeCan ensure TiAl in the melt 3 And precipitating the multi-type TiC particles coated by the intermetallic compound.
According to an embodiment of the present invention, after the second portion of the Ti source is dissolved, the alloy melt is poured into a centrifugal casting machine to obtain a Ti — Al system gradient composite material.
Preferably, the alloy melt can be first cooled to 750-850 ℃ and then heated to 950-1050 ℃. Firstly, the alloy melt is cooled to 750-850 ℃ for TiAl 3 The intermetallic compound is coated with multi-type TiC particles to be separated out, and TiAl is added when the temperature is lower than 750 DEG C 3 The precipitation size of intermetallic compounds is too large, and TiAl is generated when the temperature is higher than 850 DEG C 3 The amount of intermetallic compound precipitated is too small. Then the temperature is increased to 950 ℃ and 1050 ℃, so that TiAl can be obtained 3 The edge of the intermetallic compound is smooth, which is beneficial to the subsequent centrifugal casting process.
Preferably, after the temperature reduction and rise process is completed, the alloy melt is cooled to 780-820 ℃ again, stirring is carried out, the alloy melt is poured into a centrifugal casting machine, and the Ti-Al gradient composite material is obtained through separation, solidification and molding under the centrifugal casting condition. The centrifugal casting temperature of 780-820 ℃ is optimized, on one hand, good fluidity of the alloy melt can be ensured, the centrifugal casting process can be smoothly carried out, and on the other hand, TiAl 3 The intermetallic compound is precipitated in sufficient quantity and has good appearance, and polytype TiC particles are uniformly distributed in the intermetallic compound.
According to the embodiment of the invention, the preparation method has the advantages of low price of raw materials, low cost, high efficiency, simple and convenient operation, simple equipment, environmental protection, no pollution and strong operability, and the prepared Ti-Al gradient composite material has stable product quality, high material utilization rate and high industrialization potential.
In the following, four specific examples of the Ti — Al based gradient composite material according to the present invention are described.
Example 1
(1) The weight percentages are as follows: 0.2 wt% of carbon, 0.01 wt% of boron, 2 wt% of titanium and the balance of aluminum, and preparing the raw materials required by the Ti-Al gradient composite material: pure Al, Ti particles, Al-2C alloy and Al-3B alloy.
(2) Adding pure Al into a smelting furnace, heating to melt the pure Al to 880 ℃, heating to 930 ℃ after the pure Al is dissolved, adding Al-2C alloy and Al-3B alloy, ensuring that the mass ratio of Ti element to C element in the melt is basically 4:1, continuously standing for reaction for 15min, and stirring after the reaction is finished.
(3) Adding the rest Ti particles into the alloy melt, cooling the alloy melt to 770 ℃ after the Ti particles are dissolved, and then heating to 960 ℃.
(4) And cooling the alloy melt to 790 ℃, pouring the alloy melt into a centrifugal casting machine, stirring, separating, solidifying and molding under the centrifugal casting condition to obtain the Ti-Al gradient composite material, wherein the content of the multi-type TiC particles in the Ti-Al gradient composite material is 1 wt%.
Example 2
(1) The weight percentages are as follows: 0.4 wt% of carbon, 0.04 wt% of boron, 5 wt% of titanium and the balance of aluminum, and preparing the raw materials required by the Ti-Al gradient composite material: pure Al, Ti particles, Al-2C alloy and Al-3B alloy.
(2) Adding pure Al into a smelting furnace, heating to melt to 900 ℃, adding a first part of Ti particles into the melt, heating to 950 ℃ after dissolution, adding Al-2C alloy and Al-3B alloy, keeping the mass ratio of Ti element to C element in the melt at the moment being basically 4:1, continuously standing for reaction for 25min, and stirring after the reaction is finished.
(3) Adding the rest Ti particles into the alloy melt, cooling the alloy melt to 790 ℃ after the Ti particles are dissolved, and then heating the alloy melt to 980 ℃.
(4) And cooling the alloy melt to 795 ℃, pouring the alloy melt into a centrifugal casting machine, stirring, separating, solidifying and molding under the centrifugal casting condition to obtain the Ti-Al gradient composite material, wherein the content of the multi-type TiC particles in the Ti-Al gradient composite material is 2 wt%.
Example 3
(1) The weight percentages are as follows: 0.6 wt% of carbon, 0.04 wt% of boron, 8 wt% of titanium and the balance of aluminum, and preparing the raw materials required by the Ti-Al gradient composite material: pure Al, Ti particles, Al-2C alloy and Al-3B alloy.
(2) Adding pure Al into a smelting furnace, heating to melt to 900 ℃, adding a first part of Ti particles into the melt, heating to 1000 ℃ after dissolving, adding Al-2C alloy and Al-3B alloy, keeping the mass ratio of Ti element to C element in the melt at 4:1, continuously standing for 35min for reaction, and stirring after the reaction is finished.
(3) Adding the rest Ti particles into the alloy melt, cooling the alloy melt to 810 ℃ after the Ti particles are dissolved, and then heating to 1100 ℃.
(4) And cooling the alloy melt to 805 ℃, pouring the alloy melt into a centrifugal casting machine, stirring, separating, solidifying and forming under the centrifugal casting condition to obtain the Ti-Al gradient composite material, wherein the content of the multi-type TiC particles in the Ti-Al gradient composite material is 3 wt%. .
Example 4
(1) The weight percentages are as follows: 0.7 wt% of carbon, 0.06 wt% of boron and 8 wt% of titanium, and preparing raw materials required by the Ti-Al gradient composite material: pure Al, Ti particles, Al-2C alloy and Al-3B alloy.
(2) Adding pure aluminum into a smelting furnace, heating to melt to 920 ℃, adding a first part of Ti particles into the melt, heating to 1030 ℃ after dissolution, adding Al-2C alloy and Al-3B alloy, keeping the mass ratio of Ti element to C element in the melt at 4:1, continuously standing for reacting for 40min, and stirring after the reaction is finished.
(3) And adding the rest Ti particles into the alloy melt, cooling the alloy melt to 830 ℃ after the Ti particles are dissolved, heating to 1030 ℃, and stirring.
(4) And cooling the alloy melt to 810 ℃, pouring the alloy melt into a centrifugal casting machine, and separating, solidifying and forming under the centrifugal casting condition to obtain the Ti-Al gradient composite material, wherein the content of the multi-type TiC particles in the Ti-Al gradient composite material is 3.5 wt%. .
The Ti — Al based gradient composite material and the method for manufacturing the same according to the present invention can achieve the technical effects not limited to this description below.
According to the Ti-Al gradient composite material, the inner layer is made of aluminum alloy, the specific gravity is low, and the outer layer is made of polytype TiC reinforced TiAl 3 Intermetallic compound based composite material, thereby realizing TiAl 3 The toughening and the reinforcement of the Ti-Al series gradient composite material ensure that the Ti-Al series gradient composite material has comprehensive mechanical properties of low specific gravity, high strength and high toughness.
According to the manufacturing method of the Ti-Al gradient composite material provided by the embodiment of the invention, the adopted raw materials are low in price, low in cost, high in efficiency, simple and convenient to operate, simple in equipment, green, environment-friendly and pollution-free, and strong in operability, and the prepared Ti-Al gradient composite material is stable in product quality, high in material utilization rate and high in industrialization potential.
While exemplary embodiments of the present invention have been particularly described with reference to exemplary embodiments thereof, it will be understood by those skilled in the art that various changes in form and details may be made therein without departing from the spirit and scope of the present invention as defined by the appended claims.
Claims (10)
1. The Ti-Al gradient composite material is characterized by comprising an inner layer and an outer layer surrounding the inner layer, wherein the inner layer is aluminum alloy, and the outer layer comprises TiAl 3 Intermetallic compound and dispersed in TiAl 3 Polytype TiC particles in the intermetallic compound, the polytype TiC particles comprise B doped TiC particles formed by B atoms occupying C vacancies in TiC crystals and TiC particles not doped with B atoms.
2. The Ti-Al gradient composite material according to claim 1, wherein the amount of B doped in said B doped TiC particles is 0.1 wt% to 10 wt%.
3. The Ti-Al gradient composite material as set forth in claim 1, wherein the polytype TiC particles are contained in an amount of 0.5 wt% to 4 wt% based on 100 wt% of the Ti-Al gradient composite material, wherein the C element is 0.1 wt% to 0.8 wt%, the B element is 0.01 wt% to 0.08 wt%, the Ti element is 2 wt% to 12 wt%, and the balance is Al.
4. The Ti-Al gradient composite material as set forth in claim 1, wherein the polytype TiC particles are generated in situ and dispersed in the TiAl of the outer layer 3 An intermetallic compound matrix.
5. The Ti-Al based gradient composite of claim 1, wherein said polytype TiC particles have dual-scale features of nano-scale and micro-scale, said polytype TiC particles having a size between 20nm-1.5 μ ι η.
6. The Ti-Al based gradient composite of any of claims 1 to 5, wherein the inner layer comprises an Al matrix and the TiAl in the outer layer 3 Intermetallic compounds and the multi-type TiC particles are also contained in the Al matrix of the inner layer.
7. The method for producing a Ti-Al based gradient composite material according to any one of claims 1 to 6, comprising:
preparing raw materials, namely an Al source, a Ti source, an Al-C alloy and an Al-B alloy, and dividing the Ti source into two parts, wherein the Al-C alloy contains Al 4 C 3 The Al-B alloy includes AlB 2 ；
Adding an Al source into a smelting furnace, heating and melting to 850-950 ℃, and adding a first part of Ti source into the melt;
after the first part of Ti source is completely dissolved, heating the alloy melt to 900-1100 ℃, adding Al-C alloy and Al-B alloy, and standing for reaction for 5-45 min;
adding a second portion of the Ti source to the alloy melt and dissolving the second portion of the Ti source;
and pouring the alloy melt into a centrifugal casting machine to obtain the Ti-Al gradient composite material.
8. The manufacturing method according to claim 7, wherein the step of casting the alloy melt into a centrifugal casting machine to obtain the Ti-Al gradient composite material comprises:
cooling the alloy melt to 750-850 ℃, and then heating to 950-1050 ℃;
and cooling the alloy melt to 780-820 ℃, pouring the alloy melt into a centrifugal casting machine for separation, solidification and molding to obtain the Ti-Al gradient composite material.
9. The manufacturing method according to claim 7, wherein in the raw material, the Al source is pure aluminum, the Ti source is Ti particles, the Al-C alloy is an Al-2C alloy, the Al-B alloy is an Al-3B alloy, a weight ratio of C is 2 wt% based on the total weight of the Al-2C alloy, a weight ratio of B is 3 wt% based on the Al-3B alloy,
the raw materials were prepared according to the following ingredients contents: based on 100 wt% of the Ti-Al series gradient composite material, the mass percent of the C element is 0.1-0.8 wt%, the mass percent of the B element is 0.01-0.08 wt%, the mass percent of the Ti element is 2-12 wt%, and the balance is Al.
10. The method of claim 7, wherein the mass ratio of the Ti element to the C element in the melt after the first portion of the Ti source is added to the melt is 4: 1.
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115404373A (en) * | 2022-10-10 | 2022-11-29 | 中北大学 | Method for preparing in-situ synthesis aluminum carbide and titanium trialuminate reinforced aluminum/titanium laminated material |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07197149A (en) * | 1993-12-29 | 1995-08-01 | Toyota Motor Corp | Production of aluminum composite material containing tial3 |
| CN112410624A (en) * | 2020-11-05 | 2021-02-26 | 山东迈奥晶新材料有限公司 | Al-Si alloy, preparation method thereof and heat sink of 5G communication base station |
| CN113416861A (en) * | 2021-05-17 | 2021-09-21 | 江苏大学 | Preparation method of micro-nano dual-scale TiC particle reinforced aluminum matrix composite material |
-
2022
- 2022-05-24 CN CN202210570508.XA patent/CN114875278B/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07197149A (en) * | 1993-12-29 | 1995-08-01 | Toyota Motor Corp | Production of aluminum composite material containing tial3 |
| CN112410624A (en) * | 2020-11-05 | 2021-02-26 | 山东迈奥晶新材料有限公司 | Al-Si alloy, preparation method thereof and heat sink of 5G communication base station |
| CN113416861A (en) * | 2021-05-17 | 2021-09-21 | 江苏大学 | Preparation method of micro-nano dual-scale TiC particle reinforced aluminum matrix composite material |
Non-Patent Citations (1)
| Title |
|---|
| 杨化冰: "《中国博士学位论文全文数据库 工程科技I辑》", 15 February 2020 * |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115404373A (en) * | 2022-10-10 | 2022-11-29 | 中北大学 | Method for preparing in-situ synthesis aluminum carbide and titanium trialuminate reinforced aluminum/titanium laminated material |
| CN115404373B (en) * | 2022-10-10 | 2023-03-10 | 中北大学 | Method for preparing in-situ synthesis aluminum carbide and titanium trialuminate reinforced aluminum/titanium laminated material |
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