CN111020348A - TiC enhanced Fe prepared by combustion synthesis3Process for preparing Al composite material - Google Patents
TiC enhanced Fe prepared by combustion synthesis3Process for preparing Al composite material Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/05—Mixtures of metal powder with non-metallic powder
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
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- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/067—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds comprising a particular metallic binder
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
- C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
- C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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Abstract
The embodiment of the invention provides a method for preparing TiC reinforced Fe by combustion synthesis3The process of the Al composite material uses element powder to replace pre-alloyed powder, can obtain a tissue structure with a clean interface between a reinforcing phase and a matrix, has excellent mechanical property, and has microhardness exceeding 900HV after the composite material is prepared into a coatingEffectively improve Fe3The performance defect of the Al composite material is expanded, and Fe is expanded3The Al composite material is applied to the industrial fields of friction, wear and the like. In addition, because strategic elements and precious metals are not added, the production cost is low, the problems of long ball milling time and high-temperature annealing of powder after ball milling are solved, the process is simple, the energy consumption is low, and the efficiency is improved.
Description
Technical Field
The invention belongs to the technical field of intermetallic compounds, and particularly relates to a method for preparing TiC reinforced Fe through combustion synthesis3And (3) an Al composite material process.
Background
An intermetallic compound is a compound formed between a metal and a metal, or between a metal and a metalloid, and is a compound composed of two or more metal components in proportion having a long-range ordered crystal structure different from the constituent elements thereof and basic characteristics of the metal. The intermetallic compound has the characteristics of excellent mechanical property, high hardness, high melting point, high creep resistance and low plasticity, has good oxidation resistance and special physical and chemical properties, and is an important structural material in many fields such as aerospace, transportation, chemical engineering, machinery and the like. The ordered intermetallic compound used as high temperature structure material has excellent mechanical performance, high oxidation resistance, high corrosion resistance, high specific strength and other features, and may have both metal plasticity and ceramic high temperature strength owing to the long range ordered arrangement of atoms and the coexistence of metal bond and covalent bond.
At present, the ordered intermetallic compound used as a high-temperature structural material is mainly researched and developed at home and abroad mainly by A of three systems of Ni-Al, Ti-Al and Fe-Al3B and AB type aluminum compounds. Wherein, the Fe-Al intermetallic compound does not contain strategic elements, has low density, low cost, high strength, good wear resistance and excellent oxidation resistance, vulcanization resistance and carbonization resistance, and is a material with good wear resistance and excellent oxidation resistance, vulcanization resistance and carbonization resistanceWear-resistant materials and high-temperature structural materials with good application prospects. Fe3The Al intermetallic compound endows the material with a plurality of excellent characteristics due to the long-range ordered structure, and the corrosion resistance in the vulcanizing atmosphere is superior to that of stainless steel and anticorrosive coatings, thereby having the potential to become a practical engineering material and replace the stainless steel and the anticorrosive alloy in some occasions.
However, Fe3Al has a fatal weakness that the room temperature is brittle and the strength is sharply decreased at 600 ℃ or more, and this material has not been industrially put into practical use as a structural material. In the prior art, Cr, Mo, Nb, W, Ti and other alloy elements are added by adopting a mechanical alloying method, and Fe can be enabled to be generated by using a proper heat treatment process3The room temperature plasticity and high temperature strength of Al alloy are improved obviously, and particles such as Al are reinforced by adding synthetic ceramic2O3、WC、TiC、TiN、ZrB2、TiB2And the like can make up for the deficiency of low high-temperature strength of the alloy. However, the increase of the addition amount of the particles not only worsens the defect of low room temperature plasticity, but also causes particle agglomeration in the fusion casting process due to the increase of the particle phase, and seriously affects the mechanical properties of the material.
Disclosure of Invention
The present invention is directed to solving at least one of the problems of the prior art. Therefore, the invention provides a method for preparing TiC reinforced Fe by combustion synthesis3The process of the Al composite material uses element powder to replace pre-alloyed powder, and the prepared composite material has excellent mechanical property.
According to the embodiment of the first aspect of the invention, TiC-reinforced Fe is prepared by combustion synthesis3The process of the Al composite material comprises the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-x mol% TiC mixed powder, wherein x is more than or equal to 30 and less than or equal to 70;
s2: subjecting said Fe to3Pressing and molding the Al-xmol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain the TiC-reinforced Fe3An Al composite material.
In step S1, a sealed ball milling tank is used for ball milling, and before ball milling, vacuum pumping is performed, and argon gas is then filled for ball milling.
According to the embodiment of the invention, TiC enhanced Fe is prepared by combustion synthesis3The process of the Al composite material at least has the following technical effects:
TiC reinforced Fe prepared by combustion synthesis of the embodiment of the invention3The process of the Al composite material uses the element powder to replace the pre-alloyed powder, can obtain a tissue structure with a clean interface between a reinforcing phase and a matrix, has excellent mechanical property, and effectively improves Fe due to the fact that the microhardness exceeds 900HV after the composite material is prepared into a coating3The performance defect of the Al composite material is expanded, and Fe is expanded3The Al composite material is applied to the industrial fields of friction, wear and the like.
TiC reinforced Fe prepared by combustion synthesis of the embodiment of the invention3The process of the Al composite material has low production cost because strategic elements and noble metals are not added.
TiC reinforced Fe prepared by combustion synthesis of the embodiment of the invention3In the process of the Al composite material, ball milling in the step S1 is an effective method for activating combustion synthesis and overcoming reaction power barriers, and the ball milling time is reduced to 1/12 of mechanical alloying, so that the problems that the ball milling time is long and powder needs high-temperature annealing after ball milling are solved, the process is simple, the energy consumption is low, and the efficiency is improved.
The ball milling in step S1 is high energy ball milling. The high-energy ball milling is mechanical forced stirring ball milling, the rotating speed can be very high, the ball milling temperature is high, water cooling is needed, the ball milling impact energy is large, the efficiency is high, the ball milling time is short, the low-energy ball milling is ball milling by using a common ball mill, the efficiency is low, the time is long, and the rotating speed is low.
The high-energy ball milling and the low-energy ball milling are different not only in ball milling speed but also mainly in different principles of ball milling equipment, and stirring ball milling, vibration ball milling and planetary ball milling are generally adopted in the high-energy ball milling. Low energy ball milling generally refers to roller milling in the conventional sense.
In step S1, after the high energy ball milling, the particles have high surfacePlastic deformation strain energy, which becomes the driving force for the chemical synthesis reaction. Because of the usual mechanical alloying to produce intermetallic powders, with Fe3For example, Al is dissolved in a Fe matrix to form a supersaturated solid solution by using low-energy mechanical ball milling, and the process needs to accurately control the ball milling time because intermediate transition metastable phases such as Fe exist2Al5And FeAl2And annealing treatment is carried out subsequently to convert the metastable phase into the stable phase.
TiC reinforced Fe prepared by combustion synthesis of the embodiment of the invention3And (S3) sintering the blank in a preheated protective atmosphere, wherein the preheated protective atmosphere can ensure that the blank has a heating rate of approximately 500 ℃/min, so as to excite the combustion synthesis reaction.
TiC reinforced Fe prepared by combustion synthesis of the embodiment of the invention3The composite material prepared by the process of the Al composite material is in a spongy and porous structure, and can be easily prepared into powder for supersonic spraying, so that the production efficiency of the coating material is further improved.
According to some embodiments of the invention, the mixed powder further comprises 2 mol% of Cr powder.
According to some embodiments of the invention, the Fe3And in the Al-xmol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1.
According to some embodiments of the invention, the Fe3In the Al-xmol% TiC mixed powder, the molar ratio of Ti powder to C powder is 1: 1.
According to some embodiments of the present invention, in step S1, the time for ball milling and mixing is 30-40 min.
According to some embodiments of the present invention, in step S1, the ball-milling mixture has a ball-to-material ratio of (5-30): 1.
according to some embodiments of the present invention, in step S2, the pressure for compression molding is 200 to 300 MPa.
According to some embodiments of the invention, in step S3, the protective atmosphere is a mixed gas of argon and hydrogen.
According to some embodiments of the invention, in step S3, the sintering temperature is 1100-1200 ℃.
According to some embodiments of the invention, in the step S3, the sintering time is 2-3 min.
Detailed Description
The following are specific examples of the present invention, and the technical solutions of the present invention will be further described with reference to the examples, but the present invention is not limited to the examples.
Example 1
This example provides a method for preparing TiC reinforced Fe by combustion synthesis3The process of the Al composite material comprises the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-x mol% TiC mixed powder, wherein x is more than or equal to 30 and less than or equal to 70;
s2: subjecting said Fe to3Pressing and molding the Al-xmol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain the TiC-reinforced Fe3An Al composite material.
Wherein, Fe3And in the Al-xmol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing is 30-40 min. The ball-material ratio of ball-milling mixing is (5-30): 1. the ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for compression molding is 200-300 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The sintering temperature is 1100-1200 ℃. The sintering time is 2-3 min.
Example 2
This example provides a method for preparing TiC reinforced Fe by combustion synthesis3The process of the Al composite material comprises the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtainFe3Al-x mol% TiC mixed powder, wherein x is more than or equal to 30 and less than or equal to 70;
s2: subjecting said Fe to3Pressing and molding the Al-xmol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain the TiC-reinforced Fe3An Al composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-xmol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing is 30-40 min. The ball-material ratio of ball-milling mixing is (5-30): 1. the ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for compression molding is 200-300 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The sintering temperature is 1100-1200 ℃. The sintering time is 2-3 min.
Example 3
This example actually prepares Fe3An Al-30 mol% TiC composite material comprising the steps of:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-30 mol% TiC mixed powder;
s2: subjecting said Fe to3Pressing and molding the Al-30 mol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain Fe3Al-30 mol% TiC composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-30 mol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing was 30 min. The ball-material ratio of ball-milling mixing is 30: 1. the rotation speed of the ball mill is 380 rpm. The ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for press molding was 200 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The preheating temperature of the protective atmosphere is 1100 ℃, and the sintering temperature is 1100 ℃. The sintering time is 2-3 min.
Preparation of the resulting Fe3The Al-30 mol% TiC composite material is blocky and has a sponge and porous structure.
Example 4
This example actually prepares Fe3Al-40 mol% TiC composite material, comprising the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-40 mol% TiC mixed powder;
s2: subjecting said Fe to3Pressing and molding the Al-40 mol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain Fe3Al-40 mol% TiC composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-40 mol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing was 30 min. The ball-material ratio of ball-milling mixing is 30: 1. the rotation speed of the ball mill is 380 rpm. The ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for press molding was 200 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The preheating temperature of the protective atmosphere is 1130 ℃, and the sintering temperature is 1130 ℃. The sintering time is 2-3 min.
Preparation of the resulting Fe3The Al-40 mol% TiC composite material is blocky and has a sponge and porous structure.
Example 5
This example actually prepares Fe3An Al-50 mol% TiC composite material comprising the steps of:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-50 mol% TiC mixed powder;
s2: subjecting said Fe to3Pressing and molding the Al-500 mol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain Fe3Al-50 mol% TiC composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-50 mol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing was 30 min. The ball-material ratio of ball-milling mixing is 30: 1. the rotation speed of the ball mill is 380 rpm. The ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for press molding was 200 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The preheating temperature of the protective atmosphere is 1150 ℃, and the sintering temperature is 1150 ℃. The sintering time is 2-3 min.
Preparation of the resulting Fe3The Al-50 mol% TiC composite material is blocky and has a sponge and porous structure.
Example 6
This example actually prepares Fe3An Al-60 mol% TiC composite material, comprising the steps of:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-60 mol% TiC mixed powder;
s2: subjecting said Fe to3Pressing and molding the Al-60 mol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain Fe3Al-60 mol% TiC composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-60 mol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing was 30 min. The ball-material ratio of ball-milling mixing is 30: 1. the rotation speed of the ball mill is 380 rpm. The ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for press molding was 200 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The preheating temperature of the protective atmosphere is 1150 ℃, and the sintering temperature is 1180 ℃. The sintering time is 2-3 min.
Preparation of the resulting Fe3The Al-60 mol% TiC composite material is blocky and has a sponge and porous structure.
Example 7
This example actually prepares Fe3Al-70 mol% TiC composite material, comprising the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-70 mol% TiC mixed powder;
s2: subjecting said Fe to3Pressing and molding the Al-70 mol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain Fe3Al-70 mol% TiC composite material.
Wherein, the mixed powder also comprises 2 mol% of Cr powder.
Fe3And in the Al-60 mol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1. The molar ratio of the Ti powder to the C powder is 1: 1.
In step S1, the time for ball milling and mixing was 30 min. The ball-material ratio of ball-milling mixing is 30: 1. the rotation speed of the ball mill is 380 rpm. The ball milling adopts a sealed ball milling tank, the ball milling is firstly vacuumized before ball milling, and argon is filled for ball milling.
In step S2, the pressure for press molding was 200 MPa.
In step S3, the protective atmosphere is a mixed gas of argon and hydrogen. The preheating temperature of the protective atmosphere is 1200 ℃, and the sintering temperature is 1180 ℃. The sintering time is 2-3 min.
Preparation of the resulting Fe3The Al-70 mol% TiC composite material is blocky and has a sponge and porous structure.
Comparative example 1
This example actually prepares comparative Fe3An Al-30 mol% TiC composite material comprising the steps of:
respectively weighing Fe according to the design requirements of the components3Mixing Al powder, Ti powder and C powder to prepare Fe3Al-30 mol% TiC mixed powder. And placing the prepared mixed powder in a high-energy ball mill sealed tank, vacuumizing an argon atmosphere, and carrying out ball milling for 6 hours at a ball-material ratio of 10:1 and a ball mill rotating speed of 300 rpm. The ball-milled powder was then placed at 1000 ℃ under high vacuum (. apprxeq.10)-4Pa) for 2h to obtain comparative Fe3Al-30 mol% TiC composite powder.
Comparative example 2
This example actually prepares comparative Fe3An Al-50 mol% TiC composite material comprising the steps of:
respectively weighing Fe according to the design requirements of the components3Mixing Al powder, Ti powder and C powder to prepare Fe3Al-50 mol% TiC mixed powder. And placing the prepared mixed powder in a high-energy ball mill sealed tank, vacuumizing an argon atmosphere, and carrying out ball milling for 6 hours at a ball-material ratio of 10:1 and a ball mill rotating speed of 300 rpm. The ball-milled powder was then placed at 1050 ℃ under high vacuum (. apprxeq.10)-4Pa) for 2h to obtain comparative Fe3Al-50 mol% TiC composite powder.
Comparative example 3
This example actually prepares comparative Fe3Al-70 mol% TiC composite material, comprising the following steps:
respectively weighing Fe according to the design requirements of the components3Mixing Al powder, Ti powder and C powder to prepare Fe3Al-70 mol% TiC mixed powder. Placing the prepared mixed powder in a high-energy ball mill sealing tank, vacuumizing an argon atmosphere, and ball milling for 6 hours at a ball-to-material ratio of 10:1The rotation speed of the ball mill was 300 rpm. The ball-milled powder was then placed at 1100 ℃ under high vacuum (. apprxeq.10)-4Pa) for 2h to obtain comparative Fe3Al-70 mol% TiC composite powder.
Example of detection
In this example, the composite materials prepared in examples 3 to 5 and comparative examples 1 to 3 were prepared into supersonic spraying powder, composite coatings of corresponding numbers were prepared using a supersonic spraying apparatus of JP-8000 type, and the microhardness of the composite materials and the composite coatings was measured, and the results are shown in Table 1.
TABLE 1 microhardness test results
As can be seen from Table 1, Fe prepared by the process of the example of the present invention3Compared with comparative examples 1-3, the hardness of the Al-TiC composite material, namely the samples correspondingly numbered in examples 3-7, of the composite powder and the composite coating prepared by the process in the embodiment of the invention is increased along with the increase of the TiC content in the matrix. Compared with comparative examples 1-3 with the same content of reinforcing phase, the hardness of the composite coating prepared by the combustion synthesis method provided by the embodiment of the invention is greatly improved in mechanical property of the coating.
Claims (10)
1. TiC enhanced Fe prepared by combustion synthesis3The process of the Al composite material is characterized by comprising the following steps:
s1: weighing Fe powder, Al powder, Ti powder and C powder, uniformly mixing to obtain mixed powder, and ball-milling the mixed powder to obtain Fe3Al-x mol% TiC mixed powder, wherein x is more than or equal to 30 and less than or equal to 70;
s2: subjecting said Fe to3Pressing and molding the Al-xmol% TiC mixed powder to obtain a blank;
s3: sintering the blank in a preheated protective atmosphere, and cooling to obtain the TiC-reinforced Fe3Al composite materialAnd (5) feeding.
2. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that the mixed powder also comprises 2 mol% of Cr powder.
3. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3Process for producing an Al composite material, characterized in that said Fe3And in the Al-xmol% TiC mixed powder, the molar ratio of Fe powder to Al powder is 3: 1.
4. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3Process for producing an Al composite material, characterized in that said Fe3In the Al-xmol% TiC mixed powder, the molar ratio of Ti powder to C powder is 1: 1.
5. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that in the step S1, the ball milling and mixing time is 30-40 min.
6. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that in the step S1, the ball-material ratio of ball-milling mixing is (5-30): 1.
7. the method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that in the step S2, the pressure for compression molding is 200-300 MPa.
8. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that, in step S3, the protective atmosphere is a mixed gas of argon and hydrogen.
9. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that in the step S3, the sintering temperature is 1100-1200 ℃.
10. The method of claim 1 for TiC-enhanced Fe by combustion synthesis3The process of the Al composite material is characterized in that in the step S3, the sintering time is 2-3 min.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202010022865.3A CN111020348A (en) | 2020-01-09 | 2020-01-09 | TiC enhanced Fe prepared by combustion synthesis3Process for preparing Al composite material |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5637816A (en) * | 1995-08-22 | 1997-06-10 | Lockheed Martin Energy Systems, Inc. | Metal matrix composite of an iron aluminide and ceramic particles and method thereof |
| CN102249682A (en) * | 2011-05-16 | 2011-11-23 | 山东交通学院 | Titanium carbide ceramic composite material reinforced with ferrum and aluminium intermetallic compound and preparation method thereof |
| CN103173675A (en) * | 2011-12-23 | 2013-06-26 | 中国科学院兰州化学物理研究所 | Preparation method of ferrum-aluminum titanium carbide composite material |
| KR20160088170A (en) * | 2015-01-15 | 2016-07-25 | 전북대학교산학협력단 | TiC-FeAl HARD MATERIALS AND FABRICATING METHOD FOR THE SAME |
| CN109112331A (en) * | 2018-08-30 | 2019-01-01 | 江苏科技大学 | A kind of fabricated in situ high performance Fe3The method and its application of Al-TiC composite material |
-
2020
- 2020-01-09 CN CN202010022865.3A patent/CN111020348A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5637816A (en) * | 1995-08-22 | 1997-06-10 | Lockheed Martin Energy Systems, Inc. | Metal matrix composite of an iron aluminide and ceramic particles and method thereof |
| CN102249682A (en) * | 2011-05-16 | 2011-11-23 | 山东交通学院 | Titanium carbide ceramic composite material reinforced with ferrum and aluminium intermetallic compound and preparation method thereof |
| CN103173675A (en) * | 2011-12-23 | 2013-06-26 | 中国科学院兰州化学物理研究所 | Preparation method of ferrum-aluminum titanium carbide composite material |
| KR20160088170A (en) * | 2015-01-15 | 2016-07-25 | 전북대학교산학협력단 | TiC-FeAl HARD MATERIALS AND FABRICATING METHOD FOR THE SAME |
| CN109112331A (en) * | 2018-08-30 | 2019-01-01 | 江苏科技大学 | A kind of fabricated in situ high performance Fe3The method and its application of Al-TiC composite material |
Non-Patent Citations (2)
| Title |
|---|
| HADI GHAZANFARI ET AL.: "Characterization of dry-sliding wear of HVOF coatings made of Fe3Al powders reinforced with sub-micrometer TiC particles produced by combustion synthesis", 《SURFACE&COATINGS TECHNOLOGY》 * |
| HADI GHAZANFARI ET AL.: "Mechanically activated combustion synthesis of Fe3Al composite powders reinforced with sub-micrometer TiC particles", 《JOURNAL OF ALLOYS AND COMPOUNDS》 * |
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