CN114042912B - Method for finely controlling mechanical properties of NiAl-based composite material through powder particle size - Google Patents
Method for finely controlling mechanical properties of NiAl-based composite material through powder particle size Download PDFInfo
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- 229910000943 NiAl Inorganic materials 0.000 title claims abstract description 129
- 239000002131 composite material Substances 0.000 title claims abstract description 124
- NPXOKRUENSOPAO-UHFFFAOYSA-N Raney nickel Chemical compound [Al].[Ni] NPXOKRUENSOPAO-UHFFFAOYSA-N 0.000 title claims abstract description 116
- 239000000843 powder Substances 0.000 title claims abstract description 116
- 239000002245 particle Substances 0.000 title claims abstract description 74
- 238000000034 method Methods 0.000 title claims abstract description 24
- 238000002156 mixing Methods 0.000 claims abstract description 25
- 230000014509 gene expression Effects 0.000 claims abstract description 16
- 238000005245 sintering Methods 0.000 claims abstract description 16
- 238000001816 cooling Methods 0.000 claims abstract description 9
- 238000012216 screening Methods 0.000 claims abstract description 5
- 238000003825 pressing Methods 0.000 claims abstract description 4
- 229910045601 alloy Inorganic materials 0.000 claims description 38
- 239000000956 alloy Substances 0.000 claims description 38
- 230000006835 compression Effects 0.000 claims description 25
- 238000007906 compression Methods 0.000 claims description 25
- 239000002184 metal Substances 0.000 claims description 15
- 229910052751 metal Inorganic materials 0.000 claims description 15
- 239000013078 crystal Substances 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 13
- 238000011049 filling Methods 0.000 claims description 10
- 238000012360 testing method Methods 0.000 claims description 8
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 239000007788 liquid Substances 0.000 claims description 6
- 238000007670 refining Methods 0.000 claims description 6
- 238000011068 loading method Methods 0.000 claims description 5
- 238000002360 preparation method Methods 0.000 claims description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 4
- PCHJSUWPFVWCPO-UHFFFAOYSA-N gold Chemical compound [Au] PCHJSUWPFVWCPO-UHFFFAOYSA-N 0.000 claims description 4
- 239000010931 gold Substances 0.000 claims description 4
- 229910052737 gold Inorganic materials 0.000 claims description 4
- 229910002804 graphite Inorganic materials 0.000 claims description 4
- 239000010439 graphite Substances 0.000 claims description 4
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000000889 atomisation Methods 0.000 claims description 3
- 238000005303 weighing Methods 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims 1
- 229910000765 intermetallic Inorganic materials 0.000 abstract description 5
- 239000002994 raw material Substances 0.000 abstract description 4
- 239000000463 material Substances 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 238000007711 solidification Methods 0.000 description 2
- 230000008023 solidification Effects 0.000 description 2
- 241001085205 Prenanthella exigua Species 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000000919 ceramic Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 238000005049 combustion synthesis Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 238000001513 hot isostatic pressing Methods 0.000 description 1
- 238000007731 hot pressing Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
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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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
-
- 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
-
- 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
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
-
- 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
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
- B22F2003/1051—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding by electric discharge
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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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- 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
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0824—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid with a specific atomising fluid
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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
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
- B22F2009/0848—Melting process before atomisation
Abstract
A method for controlling the mechanical property of a NiAl-based composite material through the fine powder particle size relates to a method for controlling the mechanical property of a NiAl-based composite material. The invention aims to solve the problems that the grain size of the existing intermetallic compound NiAl is difficult to be finely controlled, the relationship between room-temperature toughness and high-temperature strength is difficult to be coordinated, and the size of the raw material can not be quickly selected through the mechanical property of the pre-obtained NiAl-based composite material. The method comprises the following steps: firstly, screening; secondly, mixing the powder; thirdly, applying pressure and maintaining pressure; fourthly, sintering; fifthly, cooling and pressure relief; sixthly, obtaining a relation A; seventhly, obtaining a relational expression B; eighthly, obtaining a relational expression C; ninthly, obtaining a relation D and a relation E. According to the invention, the mechanical property of the NiAl-based composite material can be finely controlled through the particle size of the powder; the invention can quickly select the particle size of the raw material through the mechanical property of the pre-obtained NiAl-based composite material, and the error rate is 0-2 percent.
Description
Technical Field
The invention relates to a method for controlling the mechanical property of a NiAl-based composite material.
Background
The long-range ordered intermetallic compound NiAl having the B2 structure is considered as a highly potential high-temperature structural material because of its advantages such as low density (2/3 for Ni-based high-temperature alloys), high melting point (1638 ℃), high thermal conductivity (76W/m · K), and excellent oxidation resistance. However, the low room temperature plasticity and high temperature strength of the NiAl intermetallic compound have prevented its practical use. Therefore, researchers at home and abroad adopt the processes of alloying, preparing multi-phase alloy, preparing composite material, directional solidification, mechanical alloying, hot pressing and hot isostatic pressing, combustion synthesis, microcrystalline coating and the like, and the mechanical property of the NiAl alloy is greatly improved. Among them, the preparation of a NiAl-based composite material is considered as one of the most effective methods.
The grain size has a significant influence on mechanical properties, and for room-temperature mechanical properties, the smaller the grain size, the better the room-temperature toughness, and for high-temperature mechanical properties, the smaller the grain size, the lower the high-temperature yield strength, and the opposite trends are true. For a typical high-temperature structural material, NiAl, both room-temperature toughness and high-temperature strength need to be considered, and therefore, whether to select an appropriate grain size is the key to improve the comprehensive mechanical properties. Currently, the control of the grain size is usually to control the solidification rate, heat treatment, deformation and the like, and these methods can control the range of the grain size to a certain extent, but cannot achieve fine control, so that the mechanical property is difficult to stabilize.
Disclosure of Invention
The invention aims to solve the problems that the grain size of the existing intermetallic compound NiAl is difficult to be finely controlled, the relationship between room-temperature toughness and high-temperature strength is difficult to be coordinated, and the size of a raw material cannot be quickly selected through the mechanical property of a pre-obtained NiAl-based composite material, and provides a method for finely controlling the mechanical property of the NiAl-based composite material through the powder grain size.
A method for controlling the mechanical property of a NiAl-based composite material through the fine powder particle size comprises the following steps:
firstly, screening NiAl-based composite alloy powder into 5 groups of original powder with different average grain sizes;
the average particle sizes of 5 groups of original powder in the first step are respectively 10 microns, 20 microns, 30 microns, 40 microns and 50 microns;
secondly, 5 groups of original powder with different average particle sizes are divided intoRespectively filling the powder into 5 powder mixing barrels, and respectively filling O into the 5 powder mixing barrels 2 Then 5 powder mixing barrels are respectively put on a roller ball mill for mixing powder to obtain 5 groups of fully adhered O on the surface 2 The alloy powder of (4);
respectively transferring the 5 combined gold powders into 5 moulds, respectively applying pressure and maintaining pressure, and then respectively placing the 5 moulds into a discharge plasma sintering furnace;
fourthly, electrifying and heating the discharge plasma sintering furnace, then heating to 1350 ℃, loading the pressure to 40MPa and preserving the heat;
Fifthly, closing a power supply of the discharge plasma sintering furnace, relieving pressure when the temperature is reduced to 850 ℃, naturally cooling to below 80 ℃, and taking out 5 dies to obtain 5 NiAl-based composite material sintered bodies;
sixthly, measuring the average grain sizes of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the original powder as a horizontal coordinate and the average grain size of the NiAl-based composite material sintered bodies as a vertical coordinate to obtain a relational expression A;
the relation A is: d-6.8312 + 0.2992P;
wherein D represents an average crystal grain size (. mu.m) of the sintered body of the NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
seventhly, testing the maximum compression deformation at room temperature of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the maximum compression deformation at room temperature of the NiAl-based composite material sintered bodies as a vertical coordinate, and obtaining a relational expression B;
the relation B is: u is 44.8256-0.6538D;
in the formula: u-maximum compression set at room temperature (%);
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
eighthly, testing the yield strength of 5 NiAl-based composite material sintered bodies at 1000 ℃, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the yield strength of the NiAl-based composite material sintered bodies at 1000 ℃ as a vertical coordinate, and obtaining a relational expression C;
The relation C: y is 200.7948+2.7600D +0.2576D 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
ninthly, combining the relation A with the relation B and the relation C respectively to obtain a relation D that the maximum compression deformation at room temperature of the NiAl-based composite material sintered body changes along with the average grain size of the original powder and a relation E that the yield strength at 1000 ℃ of the NiAl-based composite material sintered body changes along with the average grain size of the original powder;
the relation D is: u is 40.3594-0.1956P;
in the formula: the maximum compression deformation (%) at room temperature of the sintered body of the U-NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
the relation E is: y is 231.6699+1.8788P +0.0231P 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
p-mean particle diameter (. mu.m) of the original powder.
The principle and the advantages of the invention are as follows:
firstly, the invention utilizes the intermetallic compound with good oxidation resistance at high temperature, and Hf element is easy to react with O 2 Combined to form HfO 2 The ceramic phase is characterized in that discrete granular HfO is generated on the surface of the alloy powder 2 The three-dimensional net structure can block the further growth of crystal grains, so that each original powder grows into one crystal grain, and the fine control of the crystal grain size of the composite material is realized; further, establishing a relation between the grain size and room temperature toughness and high temperature strength, and realizing fine control of mechanical properties of the NiAl-based composite material through powder grain size;
Secondly, the invention utilizes the obstruction of the three-dimensional network structure to the growth of the crystal grains to ensure that each powder forms one crystal grain, so that the size of the crystal grains of the NiAl-based composite material can be controlled through the fine grain size of the original powder, and the mechanical property of the NiAl-based composite material can be further controlled;
thirdly, the mechanical property of the NiAl-based composite material can be controlled through the fine powder particle size;
the invention can rapidly select the particle size of the raw material through the mechanical property of the pre-obtained NiAl-based composite material, and the error rate is 0-2%.
Drawings
FIG. 1 is a microstructure view of a NiAl-based composite sintered body prepared from a raw powder having an average particle diameter of 40 μm;
FIG. 2 is a graph A as synthesized in example 1;
FIG. 3 is a curve B as synthesized in example 1;
FIG. 4 is a curve C as synthesized in example 1.
Detailed Description
The following examples further illustrate the present invention but are not to be construed as limiting the invention. Modifications and substitutions to methods, procedures, or conditions of the invention may be made without departing from the spirit of the invention.
The first embodiment is as follows: the method for controlling the mechanical property of the NiAl-based composite material through the fine powder particle size is completed according to the following steps:
Firstly, screening NiAl-based composite alloy powder into 5 groups of original powder with different average grain sizes;
the average particle sizes of 5 groups of original powder in the first step are respectively 10 microns, 20 microns, 30 microns, 40 microns and 50 microns;
respectively filling 5 groups of original powder with different average particle sizes into 5 powder mixing barrels, and respectively filling O into the 5 powder mixing barrels 2 Then 5 powder mixing barrels are respectively put on a roller ball mill for mixing powder to obtain 5 groups of fully adhered O on the surface 2 The alloy powder of (4);
respectively transferring the 5 combined gold powders into 5 moulds, respectively applying pressure and maintaining pressure, and then respectively placing the 5 moulds into a discharge plasma sintering furnace;
fourthly, electrifying and heating the discharge plasma sintering furnace, then heating to 1350 ℃, loading the pressure to 40MPa and preserving the heat;
fifthly, closing a power supply of the discharge plasma sintering furnace, relieving pressure when the temperature is reduced to 850 ℃, naturally cooling to below 80 ℃, and taking out 5 dies to obtain 5 NiAl-based composite material sintered bodies;
sixthly, measuring the average grain sizes of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the original powder as a horizontal coordinate and the average grain size of the NiAl-based composite material sintered bodies as a vertical coordinate to obtain a relational expression A;
The relation A is: d-6.8312 + 0.2992P;
wherein D represents an average crystal grain size (. mu.m) of the sintered body of the NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
seventhly, testing the maximum compression deformation at room temperature of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the maximum compression deformation at room temperature of the NiAl-based composite material sintered bodies as a vertical coordinate, and obtaining a relational expression B;
the relation B is: u is 44.8256-0.6538D;
in the formula: u-maximum compression set at room temperature (%);
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
eighthly, testing the yield strength of 5 NiAl-based composite material sintered bodies at 1000 ℃, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the yield strength of the NiAl-based composite material sintered bodies at 1000 ℃ as a vertical coordinate, and obtaining a relational expression C;
relation C: 200.7948+2.7600D +0.2576D 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
ninthly, combining the relation A with the relation B and the relation C respectively to obtain a relation D that the maximum compression deformation at room temperature of the NiAl-based composite material sintered body changes along with the average grain size of the original powder and a relation E that the yield strength at 1000 ℃ of the NiAl-based composite material sintered body changes along with the average grain size of the original powder;
The relation D is: u is 40.3594-0.1956P;
in the formula: the maximum compression deformation (%) at room temperature of the sintered body of the U-NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
the relation E is: y is 231.6699+1.8788P +0.0231P 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
p-mean particle diameter (. mu.m) of the original powder.
The second embodiment is as follows: the present embodiment differs from the present embodiment in that: the preparation method of the NiAl-based composite alloy powder in the first step comprises the following steps:
weighing metal Ni particles, Al particles and Hf particles, uniformly mixing, and then carrying out vacuum refining at 1500 ℃ for 2 times, wherein the time of each vacuum refining is 5min, so as to obtain a liquid alloy;
secondly, transferring the liquid alloy into a cylindrical die for cooling to obtain cylindrical as-cast alloy;
and thirdly, preparing the cylindrical as-cast alloy into NiAl-based composite alloy powder by adopting an argon atomization method. Other steps are the same as in the first embodiment.
The third concrete implementation mode: the present embodiment differs from the first or second embodiment in that: the purity of the metal Ni particles, the Al particles and the Hf particles in the step one is more than 99.5%. The other steps are the same as in the first or second embodiment.
The fourth concrete implementation mode is as follows: the difference between this embodiment and one of the first to third embodiments is as follows: the molar ratio of the metal Ni particles, the metal Al particles and the metal Hf particles in the first step is 1:1: 0.01. The other steps are the same as those in the first to third embodiments.
The fifth concrete implementation mode: the difference between this embodiment and one of the first to fourth embodiments is: the diameter of the cylindrical as-cast alloy in the second step is 20 mm; the powder in the third step is spherical alloy powder, and the particle size of the particles is 0-200 mu m. The other steps are the same as those in the first to fourth embodiments.
The sixth specific implementation mode: the difference between this embodiment and one of the first to fifth embodiments is that the heat-retaining time in step four is 30 min. The other steps are the same as those in the first to fifth embodiments.
The seventh embodiment: the difference between this embodiment and one of the first to sixth embodiments is: the mold in the third step is a high-strength graphite mold. The other steps are the same as those in the first to sixth embodiments.
The specific implementation mode is eight: the difference between this embodiment and one of the first to seventh embodiments is: the pressure in the third step is 10MPa, and the pressure maintaining time is 2 min. The other steps are the same as those in the first to seventh embodiments.
The specific implementation method nine: the difference between this embodiment and the first to eighth embodiments is: and the time for mixing the powder in the second step is 12 hours. The other steps are the same as those in the first to eighth embodiments.
The specific implementation mode is ten: the difference between this embodiment and one of the first to ninth embodiments is as follows: the rate of temperature rise described in step four was 100 ℃. The other steps are the same as those in the first to ninth embodiments.
The beneficial effects of the invention are verified by adopting the following experiments:
the first embodiment is as follows: a method for finely controlling the mechanical property of a NiAl-based composite material through the particle size of powder is completed according to the following steps:
firstly, screening NiAl-based composite alloy powder into 5 groups of original powder with different average grain sizes, wherein the original powder is 10 microns, 20 microns, 30 microns, 40 microns and 50 microns respectively;
respectively filling 5 groups of original powder with different average particle sizes into 5 powder mixing barrels, and respectively filling O into the 5 powder mixing barrels 2 And 5 are further addedRespectively putting the powder mixing barrels on a roller ball mill to mix the powder for 12h to obtain 5 groups of fully adhered O on the surfaces 2 The alloy powder of (4);
respectively transferring the 5 combined gold powders into 5 moulds, respectively applying 10MPa pressure and maintaining the pressure for 2min, and then respectively placing the 5 moulds into a discharge plasma sintering furnace;
The mould in the third step is a high-strength graphite mould;
fourthly, electrifying and heating the discharge plasma sintering furnace, then heating to 1350 ℃ at the heating rate of 100 ℃/min, loading the pressure to 40MPa, and preserving the heat under the conditions that the temperature is 1350 ℃ and the pressure is 40 MPa;
fifthly, closing a power supply of the discharge plasma sintering furnace, relieving pressure when the temperature is reduced to 850 ℃, naturally cooling to below 80 ℃, and taking out 5 dies to obtain 5 NiAl-based composite material sintered bodies;
sixthly, measuring the average grain sizes of the 5 sintered NiAl-based composite materials respectively, fitting a curve shown in figure 2 by taking the average grain size of the original powder as a horizontal coordinate and the average grain size of the sintered NiAl-based composite materials as a vertical coordinate, and obtaining a relational expression A;
the relation A is: d-6.8312 + 0.2992P;
wherein D represents an average crystal grain size (. mu.m) of the sintered body of the NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
seventhly, testing the maximum compression deformation at room temperature of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve shown in figure 3 by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the maximum compression deformation at room temperature of the NiAl-based composite material sintered bodies as a vertical coordinate, and obtaining a relational expression B;
The relation B is: u is 44.8256-0.6538D;
in the formula: u-maximum compression set at room temperature (%);
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
eighthly, testing the yield strength of 5 NiAl-based composite material sintered bodies at 1000 ℃, fitting a curve shown in figure 4 by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the yield strength of the NiAl-based composite material sintered bodies at 1000 ℃ as a vertical coordinate, and obtaining a relational expression C;
relation C: 200.7948+2.7600D +0.2576D 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
ninthly, combining the relation A with the relation B and the relation C respectively to obtain a relation D that the maximum compression deformation at room temperature of the NiAl-based composite material sintered body changes along with the average grain size of the original powder and a relation E that the yield strength at 1000 ℃ of the NiAl-based composite material sintered body changes along with the average grain size of the original powder;
the relation D is: u is 40.3594-0.1956P;
in the formula: the maximum compression deformation (%) at room temperature of the sintered body of the U-NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
The relation E is: y is 231.6699+1.8788P +0.0231P 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
p-mean particle diameter (. mu.m) of the original powder.
FIG. 1 is a microstructure view of a NiAl-based composite sintered body prepared from a raw powder having an average particle diameter of 40 μm;
from fig. 1 it can be seen that the NiAl-based composite material consists of a grey NiAl matrix and a bright white network structure.
FIG. 2 is a graph A as synthesized in example 1;
as can be seen from fig. 2, the relationship a between the average crystal grain size of the NiAl-based composite sintered body and the average grain size of the original powder is: d-6.8312 + 0.2992P;
wherein D represents an average crystal grain size (. mu.m) of the sintered body of the NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
FIG. 3 is a curve B as synthesized in example 1;
as can be seen from fig. 3, the relationship B between the maximum compression deformation amount at room temperature of the sintered NiAl-based composite material and the average crystal grain size of the sintered NiAl-based composite material is: u is 44.8256-0.6538D;
in the formula: u-maximum compression set at room temperature (%);
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
FIG. 4 is a curve C as fitted for example 1;
as can be seen from fig. 4, the yield strength at 1000 ℃ of the sintered NiAl-based composite material body and the average grain size of the sintered NiAl-based composite material body are expressed by the following formula C: 200.7948+2.7600D +0.2576D 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material.
Example 2: the preparation method of the NiAl-based composite material sintered body is completed according to the following steps:
firstly, respectively filling NiAl-based composite alloy powder (original powder) with the average particle size of 25 mu m into a powder mixing barrel, and respectively filling O into the powder mixing barrel 2 Respectively putting the powder mixing barrels on a roller type ball mill to mix the powder for 12 hours to obtain the powder with the surface fully adhered with O 2 The alloy powder of (4);
respectively transferring the alloy powder into moulds, respectively applying 10MPa pressure and maintaining the pressure for 2min, and then respectively placing the moulds into a discharge plasma sintering furnace;
the mould in the second step is a high-strength graphite mould;
thirdly, electrifying and heating the discharge plasma sintering furnace, then heating to 1350 ℃ at the heating rate of 100 ℃/min, loading the pressure to 40MPa, and preserving the heat under the conditions of 1350 ℃ and 40 MPa;
and fourthly, closing the power supply of the discharge plasma sintering furnace, relieving pressure when the temperature is reduced to 850 ℃, naturally cooling to below 80 ℃, and taking out the die to obtain the NiAl-based composite material sintered body.
The yield strength at 1000 ℃ of the NiAl-based composite material sintered body prepared in example two was predicted to be 423.0149MPa and the maximum compression deformation at room temperature was predicted to be 35.4694% by the relational expressions D and E; as a result of actual measurement, the yield strength at 1000 ℃ of the NiAl-based composite sintered body prepared in example two was 419.20MPa, and the maximum compression set at room temperature was 36.02%, and it was found that the error in predicting the yield strength at 1000 ℃ by using the relational expressions D and E in example one was 0.9%; the error of the maximum compression set at room temperature was 1.6%.
The preparation method of the NiAl-based composite alloy powder described in the first step of the examples 1 and 2 is as follows:
weighing metal Ni particles, Al particles and Hf particles, uniformly mixing, and then carrying out vacuum refining at 1350 ℃ for 2 times, wherein the time of each vacuum refining is 5min, so as to obtain a liquid alloy;
the purity of the metal Ni particles, the Al particles and the Hf particles in the step one is more than 99.5 percent;
the molar ratio of the metal Ni particles, the metal Al particles and the metal Hf particles in the first step is 1:1: 0.01;
secondly, transferring the liquid alloy into a cylindrical die for cooling to obtain cylindrical as-cast alloy;
the diameter of the cylindrical as-cast alloy in the second step is 20 mm;
thirdly, preparing the cylindrical as-cast alloy into NiAl-based composite alloy powder by adopting an argon atomization method;
the powder in the third step is spherical alloy powder, and the particle size of the particles is 0-200 mu m.
Claims (7)
1. A method for controlling the mechanical property of a NiAl-based composite material through the fine powder particle size is characterized in that the method for controlling the mechanical property of the NiAl-based composite material through the fine powder particle size is completed according to the following steps:
firstly, screening NiAl-based composite alloy powder into 5 groups of original powder with different average grain sizes;
The average particle sizes of 5 groups of original powder in the first step are respectively 10 microns, 20 microns, 30 microns, 40 microns and 50 microns;
the preparation method of the NiAl-based composite alloy powder in the first step comprises the following steps:
weighing metal Ni particles, Al particles and Hf particles, uniformly mixing, and then carrying out vacuum refining at 1500 ℃ for 2 times, wherein the time of each vacuum refining is 5min, so as to obtain a liquid alloy;
the molar ratio of the metal Ni particles, the metal Al particles and the metal Hf particles in the step I is 1:1: 0.01;
secondly, transferring the liquid alloy into a cylindrical die for cooling to obtain cylindrical as-cast alloy;
the diameter of the cylindrical as-cast alloy in the step II is 20 mm;
preparing the cylindrical as-cast alloy into NiAl-based composite alloy powder by adopting an argon atomization method;
the powder in the third step is spherical alloy powder, and the particle size of the particles is 0-200 mu m;
respectively filling 5 groups of original powder with different average particle sizes into 5 powder mixing barrels, and respectively filling O into the 5 powder mixing barrels 2 Then 5 powder mixing barrels are respectively put on a roller ball mill for mixing powder to obtain 5 groups of fully adhered O on the surface 2 The alloy powder of (4);
the time for mixing the powder in the second step is 12 hours;
respectively transferring the 5 combined gold powders into 5 moulds, respectively applying pressure and maintaining pressure, and then respectively placing the 5 moulds into a discharge plasma sintering furnace;
Fourthly, electrifying and heating the discharge plasma sintering furnace, then heating to 1350 ℃, loading the pressure to 40MPa and preserving the heat;
fifthly, closing a power supply of the discharge plasma sintering furnace, relieving pressure when the temperature is reduced to 850 ℃, naturally cooling to below 80 ℃, and taking out 5 dies to obtain 5 NiAl-based composite material sintered bodies;
sixthly, measuring the average grain sizes of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the original powder as a horizontal coordinate and the average grain size of the NiAl-based composite material sintered bodies as a vertical coordinate to obtain a relational expression A;
the relation A is: d-6.8312 + 0.2992P;
wherein D represents an average crystal grain size (. mu.m) of the sintered body of the NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
seventhly, testing the maximum compression deformation at room temperature of the 5 NiAl-based composite material sintered bodies respectively, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the maximum compression deformation at room temperature of the NiAl-based composite material sintered bodies as a vertical coordinate, and obtaining a relational expression B;
the relation B is: u is 44.8256-0.6538D;
in the formula: u-maximum compression set at room temperature (%);
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
Eighthly, testing the yield strength of 5 NiAl-based composite material sintered bodies at 1000 ℃, fitting a curve by taking the average grain size of the NiAl-based composite material sintered bodies as a horizontal coordinate and the yield strength of the NiAl-based composite material sintered bodies at 1000 ℃ as a vertical coordinate, and obtaining a relational expression C;
the relation C: 200.7948+2.7600D +0.2576D 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
d-average grain size (. mu.m) of the sintered body of the NiAl-based composite material;
ninthly, combining the relation A with the relation B and the relation C respectively to obtain a relation D that the maximum compression deformation at room temperature of the NiAl-based composite material sintered body changes along with the average grain size of the original powder and a relation E that the yield strength at 1000 ℃ of the NiAl-based composite material sintered body changes along with the average grain size of the original powder;
the relation D is: u is 40.3594-0.1956P;
in the formula: the maximum compression deformation (%) at room temperature of the sintered body of the U-NiAl-based composite material;
p-mean particle size (. mu.m) of the original powder;
the relation E is: y is 231.6699+1.8788P +0.0231P 2 ；
In the formula: yield strength (MPa) at 1000 ℃ of the Y-NiAl-based composite material sintered body;
p-mean particle diameter (. mu.m) of the original powder.
2. The method for controlling the mechanical property of the NiAl-based composite material through the fine powder particle size as claimed in claim 1, wherein the purity of the metal Ni particles, the Al particles and the Hf particles in the step (r) is more than 99.5%.
3. The method for controlling the mechanical property of the NiAl-based composite material through the fine powder particle size according to claim 1, wherein the heat preservation time in the fourth step is 30 min.
4. The method for controlling the mechanical properties of the NiAl-based composite material through the fine powder particle size according to claim 1, wherein the mold in the third step is a high-strength graphite mold.
5. The method for controlling the mechanical properties of NiAl-based composite material through the fine powder particle size according to claim 1, wherein the pressure in step three is 10MPa, and the pressure maintaining time is 2 min.
6. The method for controlling the mechanical properties of the NiAl-based composite material through the fine powder particle size as claimed in claim 1, wherein the time for mixing the powder in the second step is 12 hours.
7. The method for controlling mechanical properties of NiAl-based composite material through fine powder particle size according to claim 1, wherein the temperature increase rate in step four is 100 ℃.
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Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106498898A (en) * | 2016-11-22 | 2017-03-15 | 河海大学 | A kind of earth and stone material Gradation Optimization method based on fractal theory and physical mechanics test |
| CN109868381A (en) * | 2017-12-04 | 2019-06-11 | 北京有色金属研究总院 | A kind of preparation method of high-volume fractional tungsten particle reinforced aluminum matrix composites |
| CN111455204A (en) * | 2020-04-29 | 2020-07-28 | 哈尔滨工业大学 | Method for preparing NiAl intermetallic compound |
| CN111471896A (en) * | 2020-05-14 | 2020-07-31 | 哈尔滨工业大学 | Preparation method of nano hafnium oxide reinforced NiAl composite material |
| CN113343516A (en) * | 2021-05-14 | 2021-09-03 | 华中科技大学 | Method for eliminating critical deformation of powder superalloy PPB and determining extrusion process parameters |
| CN113515868A (en) * | 2021-08-04 | 2021-10-19 | 常熟理工学院 | Chain cluster model construction method and performance estimation method of magnetorheological elastomer |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AU1781399A (en) * | 1999-01-06 | 2000-07-24 | Ceramight Composites Ltd. | Metal-ceramic laminar-band composite |
| EP1546056B1 (en) * | 2002-07-19 | 2013-12-11 | PPG Industries Ohio, Inc. | Article having nano-scaled structures and a process for making such article |
| CN101143790B (en) * | 2007-09-13 | 2010-10-20 | 中国海洋大学 | Gel injection moulding forming technique for boron carbide-metal composite material |
| US20220111560A9 (en) * | 2014-04-08 | 2022-04-14 | Applied Cavitation, Inc. | Systems and methods for producing materials suitable for additive manufacturing using a hydrodynamic cavitation apparatus |
| CN109207765A (en) * | 2018-10-31 | 2019-01-15 | 中国科学院金属研究所 | The method that power forging prepares oxide-dispersed alloy |
| CN109382510B (en) * | 2018-11-12 | 2021-10-08 | 五邑大学 | High-temperature alloy metal powder for 3D printing and preparation method thereof |
| CN110078481A (en) * | 2019-04-29 | 2019-08-02 | 西安交通大学 | A method of high solid loading, low viscosity ceramic slurry are prepared using aspherical ceramic particle |
| CN112176212B (en) * | 2020-09-25 | 2022-03-01 | 上海交通大学 | Composite material with in-situ synthesized particles and preparation method thereof |
-
2021
- 2021-11-12 CN CN202111341935.2A patent/CN114042912B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN106498898A (en) * | 2016-11-22 | 2017-03-15 | 河海大学 | A kind of earth and stone material Gradation Optimization method based on fractal theory and physical mechanics test |
| CN109868381A (en) * | 2017-12-04 | 2019-06-11 | 北京有色金属研究总院 | A kind of preparation method of high-volume fractional tungsten particle reinforced aluminum matrix composites |
| CN111455204A (en) * | 2020-04-29 | 2020-07-28 | 哈尔滨工业大学 | Method for preparing NiAl intermetallic compound |
| CN111471896A (en) * | 2020-05-14 | 2020-07-31 | 哈尔滨工业大学 | Preparation method of nano hafnium oxide reinforced NiAl composite material |
| CN113343516A (en) * | 2021-05-14 | 2021-09-03 | 华中科技大学 | Method for eliminating critical deformation of powder superalloy PPB and determining extrusion process parameters |
| CN113515868A (en) * | 2021-08-04 | 2021-10-19 | 常熟理工学院 | Chain cluster model construction method and performance estimation method of magnetorheological elastomer |
Non-Patent Citations (3)
| Title |
|---|
| Preparation and properties of Nano-HfO2 reinforced NiAl intermetallics fabricated with powder metallurgy;Zhen Lu;《Materials Science & Engineering A》;20201130;1-10 * |
| 渐变曲率Inconel718厚板热弯曲成形精度与表面质量控制;高鹏;《航空材料学报》;20120630;61-67 * |
| 粉末粒径对热压烧结碳化硼致密化及力学性能的影响;杜贤武;《无机材料学报》;20131031;1062-1066 * |
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