CN105734324A - Preparing method for powder metallurgy high-entropy alloy based composite material - Google Patents
Preparing method for powder metallurgy high-entropy alloy based composite material Download PDFInfo
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 94
- 239000000956 alloy Substances 0.000 title claims abstract description 94
- 239000002131 composite material Substances 0.000 title claims abstract description 74
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 36
- 238000000034 method Methods 0.000 title claims abstract description 30
- 239000000843 powder Substances 0.000 claims abstract description 80
- 238000005245 sintering Methods 0.000 claims abstract description 55
- 229910033181 TiB2 Inorganic materials 0.000 claims abstract description 32
- 239000011159 matrix material Substances 0.000 claims abstract description 19
- 239000000463 material Substances 0.000 claims abstract description 16
- 238000000465 moulding Methods 0.000 claims abstract description 16
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 claims abstract description 14
- 238000000889 atomisation Methods 0.000 claims abstract description 12
- 229910052751 metal Inorganic materials 0.000 claims abstract description 10
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 35
- 239000011651 chromium Substances 0.000 claims description 35
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 33
- 239000000203 mixture Substances 0.000 claims description 31
- 238000002360 preparation method Methods 0.000 claims description 31
- 239000010949 copper Substances 0.000 claims description 18
- 239000010936 titanium Substances 0.000 claims description 18
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 16
- 239000007789 gas Substances 0.000 claims description 12
- 238000001816 cooling Methods 0.000 claims description 9
- 229910052786 argon Inorganic materials 0.000 claims description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 230000002708 enhancing effect Effects 0.000 claims description 5
- 229910052759 nickel Inorganic materials 0.000 claims description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 229910052756 noble gas Inorganic materials 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 3
- 229910017052 cobalt Inorganic materials 0.000 claims description 3
- 239000010941 cobalt Substances 0.000 claims description 3
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 3
- 229910052802 copper Inorganic materials 0.000 claims description 3
- 238000005728 strengthening Methods 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 2
- 230000004927 fusion Effects 0.000 claims description 2
- 229910052757 nitrogen Inorganic materials 0.000 claims description 2
- 239000002245 particle Substances 0.000 claims description 2
- 230000001681 protective effect Effects 0.000 claims description 2
- 230000002787 reinforcement Effects 0.000 abstract description 12
- 239000002994 raw material Substances 0.000 abstract description 11
- 239000006104 solid solution Substances 0.000 abstract description 8
- 238000005260 corrosion Methods 0.000 abstract description 5
- 239000002184 metal Substances 0.000 abstract description 5
- 230000007797 corrosion Effects 0.000 abstract description 4
- 238000002156 mixing Methods 0.000 abstract description 3
- 238000009776 industrial production Methods 0.000 abstract description 2
- 239000004615 ingredient Substances 0.000 abstract description 2
- 238000007599 discharging Methods 0.000 abstract 1
- 238000009689 gas atomisation Methods 0.000 abstract 1
- 238000002844 melting Methods 0.000 description 10
- 230000008018 melting Effects 0.000 description 10
- 230000006698 induction Effects 0.000 description 8
- 239000007769 metal material Substances 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 4
- 230000000694 effects Effects 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 2
- 238000009792 diffusion process Methods 0.000 description 2
- 238000010891 electric arc Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910000905 alloy phase Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007812 deficiency Effects 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000000280 densification Methods 0.000 description 1
- 230000005611 electricity Effects 0.000 description 1
- 239000008187 granular material Substances 0.000 description 1
- 229910002804 graphite Inorganic materials 0.000 description 1
- 239000010439 graphite Substances 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- -1 phase Al Chemical class 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 238000007789 sealing Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000002490 spark plasma sintering Methods 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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
-
- 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
- B22F9/06—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
- C22C30/00—Alloys containing less than 50% by weight of each constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—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 borides
-
- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/25—Process efficiency
Abstract
The invention relates to a preparing method for a powder metallurgy high-entropy alloy based composite material, and belongs to the field of powder metallurgy materials. The preparing method includes the steps that all components are prepared and taken according to component proportions of a designed high-entropy alloy matrix, and high-entropy alloy powder is prepared through a gas atomization method; and then according to the component proportions of the designed high-entropy alloy based composite material, the high-entropy alloy powder and wild phase titanium diboride powder are prepared and taken, and rapid sintering molding is achieved after even mixing is carried out. According to the preparing method, the atomization method is adopted for preparing spherical high-entropy alloy powder with relatively-even ingredients in advance, and therefore a simple solid solution phase structure of a high-entropy alloy is guaranteed; and discharging plasma rapid sintering is adopted for preparing the needed powder metallurgy high-entropy alloy based composite material, and therefore the shortcoming that the material is prepared with metal powder as a raw material through a powder metallurgy method traditionally, and consequently the high-entropy alloy of the simple solid solution structure is difficult to obtain is overcome. The preparing method is simple in process procedure; according to the prepared powder metallurgy high-entropy alloy based composite material, titanium diboride is evenly distributed, reinforcement and base body interface bonding is better, the comprehensive performance is more excellent, the specific strength is high, the specific rigidity is high, and the abrasive resistance and the corrosion resistance are excellent. The preparing method is suitable for industrial production.
Description
Technical field
The preparation method that the present invention relates to a kind of powder metallurgy high-entropy alloy-base composite material.Belong to technical field of powder metallurgy material preparation.
Background technology
High-entropy alloy is using five kinds or more than five kinds metals as essential element, the molar fraction of every kind of element is between 5% to 35%, there is simple solid solution phase structure, such as face-centred cubic structure (FCC) phase, unordered body-centered cubic structure (BCC) phase, orderly body-centered cubic structure (B2) phase or close-packed hexagonal structure (HCP) phase.Owing to high-entropy alloy has high entropy, big distortion of lattice, the slowly feature such as diffusion and Cocktail effect, alloy is made to present simple solid solution phase structure in microstructure, and performance shows as high intensity/hardness and hardening property, high temperature oxidation resisting and softening, there is good wearability and corrosion resistance, its combination property is significantly more than traditional metal material, thus is paid close attention to widely.The solid solution phase of composition high-entropy alloy is by simple face-centred cubic structure (FCC) phase, unordered body-centered cubic structure (BCC) phase, orderly body-centered cubic structure (B2) phase or close-packed hexagonal structure (HCP) phase composition, the composition of alloy mainly includes the high-entropy alloy containing Al or the high-entropy alloy without Al, the former mainly by FCC phase, BCC phase, B2 is equal forms heterogeneous structure, has high intensity/hardness, the feature such as wear-resisting and high temperature resistant；And the latter is by single FCC phase composition, there is the advantages such as good, the corrosion-resistant and good processing characteristics of Toughness, but the room temperature strength of alloy is relatively on the low side, it is necessary to further following process is to improve intensity.Powder metallurgy high-entropy alloy-base composite material is using high-entropy alloy as matrix phase, add other granule as reinforcement, this composite material has high-strength/high-ductility, high temperature resistant anti-softening and good corrosion resisting property, is expected to become a new generation's thermal structure and functional material.Titanium diboride (TiB2) there is the advantages such as high intensity, high elastic modulus and electric-conductivity heat-conductivity high, it is widely applied at traditional metal-base composites, significantly improves the strength and toughness of metal-base composites.
Chinese patent (application number: 200810063807.4,2008 years) develops a kind of with TiB2For strengthening the high-entropy alloy-base composite material of phase, its preparation method includes adopting electric arc melting, induction melting, self-propagating-founding or powder metallurgical technique manufacture etc., wherein electricity electric arc melting, induction melting, three kinds of methods such as self-propagating-founding are uniformly that the matrix material fusing of composition high-entropy alloy is become liquid, then pass through interpolation reinforcement to stirring casting molding in melt, these method ubiquities the uneven components of the high-entropy alloy matrix in composite, serious dendritic segregation occurs, and reuniting occurs in reinforcement, skewness, reaction in various degree can be there is between matrix phase and reinforcement simultaneously, cause that harmful phase occurs in the interface between the matrix of composite and reinforcement, reduce the intensity of composite；And adopting powder metallurgical technique to prepare high-entropy alloy-base composite material, the method is: (1) is TiB2Strengthen the metals such as phase Al, Cu, Ni, Co, Ti with composition high-entropy alloy and weigh each element powders raw material sealing mix homogeneously in proportion, be then pressed into block, then be cold-pressed into prefabricated section；(2) prefabricated section of colding pressing dries, degasification, is then placed in graphite jig and carries out hot pressed sintering 2h, and stove is cold obtains composite.The method adopts each elemental metal powders raw material composition high-entropy alloy and reinforcement TiB2Mixing hot pressed sintering, preparation technology is long, it is difficult to the matrix of guarantee composite is high-purity high-entropy alloy, and the fusing point because forming each metallic element of high-entropy alloy is different from activity, in the high-temperature sintering process of long period, TiB2Can there is reaction in various degree in reinforcement and each metallic element of matrix, it is difficult to control the phase composition of composite.
Still do not adopt spherical high-entropy alloy powder prepared by atomization as matrix phase raw material at present, prepare, by discharge plasma sintering method, the powder metallurgy high-entropy alloy-base composite material that titanium diboride strengthens.
Summary of the invention
The purpose of the present invention is intended to the deficiency overcoming prior art, and provides a kind of technique simple, the preparation method of easy to operate powder metallurgy high-entropy alloy-base composite material.Powder metallurgy high-entropy alloy-base composite material prepared by the present invention has higher consistency, and reinforcement is evenly distributed and basal body interface is well combined, product quality high comprehensive performance.
The purpose of the present invention is achieved through the following technical solutions:
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, described high-entropy alloy-base composite material is by high-entropy alloy matrix and enhancing phase composition；First, join by the component proportion of the high-entropy alloy matrix of design and take each component, adopt atomization to prepare high-entropy alloy powder；Then, by the high-entropy alloy-base composite material component proportion of design, join and take high-entropy alloy powder and strengthen phase powder, after mix homogeneously, Fast Sintering molding.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, comprises the steps:
The first step: the preparation of high-entropy alloy powder
By the component proportion of the high-entropy alloy matrix of design, join after taking each component, add heat fusing, under protective atmosphere, adopt atomization to prepare spherical high-entropy alloy powder；
Second step: sinter molding
By the high-entropy alloy-base composite material component proportion of design, join and take the high-entropy alloy powder that enhancing phase powder obtains with the first step, after mix homogeneously, adopt discharge plasma sintering molding, sintering process parameter is: sintering temperature 1000～1300 DEG C, sintering time 5～15min, pressure 30～60MPa.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, described high-entropy alloy-base composite material includes following component, by volume percentage ratio composition:
High-entropy alloy powder 55～95%,
Titanium diboride 5%～45%.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, described high-entropy alloy powder includes following component, by mole composition:
Aluminum 15～25%,
Ferrum 15～25%,
Chromium 15～25%,
Cobalt 15～25%,
Nickel 15～25%.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, described high-entropy alloy powder includes following component, by mole composition:
Aluminum 15～25%,
Ferrum 15～25%,
Chromium 15～25%,
Cobalt 15～25%,
Nickel 15～25%,
Copper 0～10%,
Titanium 0～10%.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, in the first step, in high-entropy alloy matrix component, each component is with the form dispensing of its metallic element block materials.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, in the first step, adopts intermediate frequency furnace to heat to fusion temperature 1600～2000 DEG C；Being atomized using noble gas as atomization gas, gas flow is 80～200L/s, and rate of cooling is 104K/s～106K/s, prepares spherical high-entropy alloy powder, and high-entropy alloy powder particle mean size is 50～1 microns；Noble gas is selected from nitrogen or argon, and atomization pressure is 3～6Mpa, by controlling gas flow, gas pressure and rate of cooling, makes the powder sphericity controlled diameter of high-entropy alloy.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, in second step, strengthening is titanium diboride mutually, and granularity is 10～1 microns.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, in second step, strengthens phase powder and adopts V-type batch mixer or ball mill to mix homogeneously with high-entropy alloy powder.
The preparation method of a kind of powder metallurgy high-entropy alloy-base composite material of the present invention, the comprcssive strength of the high-entropy alloy-base composite material of preparation reaches at 2250～2850MPa, and yield strength reaches at 1500～2315MPa, and consistency is 99%～99.8%.
The advantage of this technique is in that by the previously prepared one-tenth structure of atomization and phase composition stable spherical high-entropy alloy powder, then pass through discharge plasma sintering process, obtain the powder metallurgy high-entropy alloy-base composite material that high fine and close and high comprehensive performance titanium diboride strengthens, meet the requirement of actual industrial production.
The present invention adopt atomization previously prepared go out the uniform spherical high-entropy alloy powder of comparison of ingredients, it is ensured that the simple solid solution phase structure of high-entropy alloy, then, by spherical high-entropy alloy powder and TiB2Mixing, by the high-entropy alloy-base composite material that discharge plasma sintering obtains, overcoming traditional employing metal powder is that raw material is prepared by powder metallurgy process, it is difficult to the shortcoming obtaining simple solid solution structure high-entropy alloy.Simultaneously by adopting discharge plasma sintering process, Fast Sintering molding, titanium diboride is evenly distributed, reinforcement is combined with basal body interface better, combination property is more excellent in acquisition, compared with prior art, the present invention is by the spherical high-entropy alloy powder of the heterogeneous phase structure of previously prepared one-tenth and distributed components, then again through fast spark plasma sintering process, the composite element that titanium diboride reinforcement is evenly distributed, reinforcement is combined better, combination property is more excellent is prepared into high-entropy alloy basal body interface.The comprcssive strength of sintered body composite reaches 2850MPa, and yield strength reaches 2315MPa, and consistency reaches 99.8%.Requirement suitable in Aero-Space, sophisticated and futuristic weapons system, the contour ratio of automobile engine specific rigidity strong, high and wear-corrosion resistance.Be suitable to industrialized production.
Accompanying drawing illustrates:
Accompanying drawing 1 is the spherical high-entropy alloy powder shape appearance figure of the present invention.
Accompanying drawing 2 is the spherical high-entropy alloy powder X-ray diffractogram of the present invention.
Accompanying drawing 3 is the scanning electron microscope (SEM) photograph of the powder metallurgy high-entropy alloy-base composite material of the titanium diboride enhancing of the present invention.
The scanning electron microscope (SEM) photograph of the high-entropy alloy-base composite material that accompanying drawing 4 is prepared for comparative example.
From accompanying drawing 2 it can be seen that spherical powder is entirely the high-entropy alloy powder of simple solid solution structure.
From accompanying drawing 3 it can be seen that after plasma agglomeration, matrix alloy keeps spherical structure, and titanium diboride strengthens Dispersed precipitate on crystal boundary, plays Diffusion Weighting effect.
From accompanying drawing 4 it can be seen that the material adopting the method for comparative example 1 to prepare, there is obvious hole, the composition of phase is complicated, and high-entropy alloy matrix forms lower than 90%, thus reducing the bulk strength of material.
Detailed description of the invention
Method in conjunction with the present invention provides following instance:
Below embodiments of the invention are elaborated, the present embodiment premised on present invention below technical scheme under be carried out, give detailed embodiment and specific operation process.By comparing with comparative example, demonstrate and adopt composite prepared by the present invention to have high intensity and height densification feature, the comprcssive strength of the high-entropy alloy-base composite material of preparation reaches at 2250～2850MPa, and yield strength reaches at 1500～2315MPa, and consistency is at 99%-99.8%.
Comparative example 1
Preparing into volume fraction is 5%TiB2The Al strengthened20Fe20Cr20Co20Ni20High-entropy alloy-base composite material.The TiB that diameter is 5 microns2Powder, diameter are the metallic element powder such as Al, Fe, Cr, Co, Ni of 10 microns, mix homogeneously on ball mill, then sinter molding in vacuum sintering funace, sintering temperature 1300 degree, sintering pressure 5MPa, sintering time 2h, the incompressible intensity of the composite after sintering is 1520MPa, yield strength 980MPa, and material density is 91%, containing complicated composition phase in material, wherein the volume fraction of high-entropy alloy phase only has 85%.
Embodiment 1
Preparing into volume fraction is 5%TiB2The Al strengthened20Fe20Cr20Co20Ni20High-entropy alloy-base composite material.1) spherical Al is prepared20Fe20Cr20Co20Ni20High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co and high-purity N i, being fused into melt at medium frequency induction melting furnace 1600 DEG C, melt is 200L/s, pressure in throughput is the high-purity argon gas of 6MPa, 106The spherical high-entropy alloy powder of diameter 30～1 microns it is atomized under K/s rate of cooling.2) according to volume fraction 5%TiB2And 95%Al20Fe20Cr20Co20Ni20High-entropy alloy weighs the TiB that average diameter is 1 micron2The equal diameter of powder peace is 10 microns of Al20Fe20Cr20Co20Ni20High-entropy alloy powder, powder is mix homogeneously on ball mill, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1000 DEG C, and sintering pressure is 30MPa, sintering time 10min.The incompressible intensity of the composite after sintering reaches 2400MPa, and yield strength reaches 1500MPa, and the consistency of material reaches 99%.
Embodiment 2
Preparing into volume fraction is 25%TiB2The Al strengthened25Fe15Cr15Co15Ni20Ti5Cu5High-entropy alloy-base composite material.1) spherical Al is prepared25Fe15Cr15Co15Ni20Ti5Cu5High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co, high-purity N i, high-purity Ti and high-purity Cu, it is fused into melt at medium frequency induction melting furnace 1800 DEG C, melt is 80L/s, pressure in throughput is the high-purity argon gas of 4.5MPa, 104The spherical high-entropy alloy powder of diameter 50～5 microns it is atomized under K/s rate of cooling.2) according to volume fraction 25%TiB2And 75%Al25Fe15Cr15Co15Ni20Ti5Cu5High-entropy alloy weighs the TiB that average diameter is 10 microns2The equal diameter of powder peace is the Al of 20 microns25Fe15Cr15Co15Ni20Ti5Cu5High-entropy alloy powder, powder is mix homogeneously on ball mill, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1300 DEG C, and sintering pressure is 45MPa, sintering time 15min.The incompressible intensity of the composite after sintering reaches 2630MPa, and yield strength reaches 1850MPa, and the consistency of material reaches 99.4%.
Embodiment 3
Preparing into volume fraction is 20%TiB2The Al strengthened15Fe25Cr20Co15Ni15Ti10High-entropy alloy-base composite material.1) spherical Al is prepared15Fe25Cr20Co15Ni15Ti10High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co, high-purity N i and high-purity Ti, it is fused into melt at medium frequency induction melting furnace 2000 DEG C, melt is 140L/s, pressure in throughput is the high-purity argon gas of 6MPa, 105The spherical high-entropy alloy powder of diameter 40～1 microns it is atomized under K/s rate of cooling.2) according to volume fraction 20%TiB2And 80%Al15Fe25Cr20Co15Ni15Ti10High-entropy alloy weighs the TiB that average diameter is 5 microns2The equal diameter of powder peace is 15 microns of Al15Fe25Cr20Co15Ni15Ti10High-entropy alloy powder, powder is mix homogeneously on ball mill, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1200 DEG C, and sintering pressure is 60MPa, sintering time 10min.The incompressible intensity of the composite after sintering reaches 2550MPa, and yield strength reaches 2130MPa, and the consistency of material reaches 99.8%.
Embodiment 4
Preparing into volume fraction is 30%TiB2The Al strengthened15Fe20Cr25Co20Ni15Cu5High-entropy alloy-base composite material.1) spherical Al is prepared15Fe20Cr25Co20Ni15Cu5High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co, high-purity N i and high-purity Cu, it is fused into melt at medium frequency induction melting furnace 1650 DEG C, melt is 100L/s, pressure in throughput is the high-purity argon gas of 3MPa, 104The spherical high-entropy alloy powder of diameter 50～10 microns it is atomized under K/s rate of cooling.2) according to volume fraction 30%TiB2And 70%Al15Fe20Cr25Co20Ni15Cu5High-entropy alloy weighs the TiB that average diameter is 7 microns2The equal diameter of powder peace is the Al of 30 microns15Fe20Cr25Co20Ni15Cu5High-entropy alloy powder, powder is mix homogeneously on V-type machine, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1100 DEG C, and sintering pressure is 30MPa, sintering time 5min.The incompressible intensity of the composite after sintering reaches 2250MPa, and yield strength reaches 1760MPa, and the consistency of material reaches 99.0%.
Embodiment 5
Preparing into volume fraction is 45%TiB2The Al strengthened15Fe15Cr15Co25Ni25Ti5High-entropy alloy-base composite material.1) spherical Al is prepared15Fe15Cr15Co25Ni25Ti5High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co, high-purity N i and high-purity Ti, it is fused into melt at medium frequency induction melting furnace 1900 DEG C, melt is 120L/s, pressure in throughput is the high-purity argon gas of 5MPa, 105The spherical high-entropy alloy powder of diameter 40～1 microns it is atomized under K/s rate of cooling.2) according to volume fraction 45%TiB2And 55%Al15Fe15Cr15Co25Ni25Ti5High-entropy alloy weighs the TiB that average diameter is 5 microns2The equal diameter of powder peace is the Al of 25 microns15Fe15Cr15Co25Ni25Ti5High-entropy alloy powder, powder is mix homogeneously on ball mill, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1300 DEG C, and sintering pressure is 60MPa, sintering time 15min.The incompressible intensity of the composite after sintering reaches 2850MPa, and yield strength reaches 2315MPa, and the consistency of material reaches 99.7%.
Embodiment 6
Preparing into volume fraction is 30%TiB2The Al strengthened20Fe15Cr15Co20Ni20Cu10High-entropy alloy-base composite material.1) spherical Al is prepared20Fe15Cr15Co20Ni20Cu10High-entropy alloy powder (molar fraction), raw material adopts the bulk metal materials such as high-purity Al, high-purity Fe, high-purity Cr, high-purity Co, high-purity N i and high-purity Cu, it is fused into melt at medium frequency induction melting furnace 1700 DEG C, melt is 100L/s, pressure in throughput is the high-purity argon gas of 5MPa, 104The spherical high-entropy alloy powder of diameter 50～1 microns it is atomized under K/s rate of cooling.2) according to volume fraction 30%TiB2And 70%Al20Fe15Cr15Co20Ni20Cu10High-entropy alloy weighs the TiB that average diameter is 2.5 microns2The equal diameter of powder peace is the Al of 50 microns20Fe15Cr15Co20Ni20Cu10High-entropy alloy powder, powder is mix homogeneously on ball mill, then sinter molding in FCT-HPD25 discharge plasma sintering, and sintering temperature is 1250 DEG C, and sintering pressure is 45MPa, sintering time 10min.The incompressible intensity of the composite after sintering reaches 2670MPa, and yield strength reaches 1950MPa, and the consistency of material reaches 99.4%.
Claims (10)
1. a preparation method for powder metallurgy high-entropy alloy-base composite material, described high-entropy alloy-base composite material is by high-entropy alloy matrix and enhancing phase composition；First, join by the component proportion of the high-entropy alloy matrix of design and take each component, adopt atomization to prepare high-entropy alloy powder；Then, by the high-entropy alloy-base composite material component proportion of design, join and take high-entropy alloy powder and strengthen phase powder, after mix homogeneously, Fast Sintering molding.
2. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 1, comprises the steps:
The first step: the preparation of high-entropy alloy powder
By the component proportion of the high-entropy alloy matrix of design, join after taking each component, add heat fusing, under protective atmosphere, adopt atomization to prepare high-entropy alloy powder；
Second step: sinter molding
By the high-entropy alloy-base composite material component proportion of design, join and take the high-entropy alloy powder that enhancing phase powder obtains with the first step, after mix homogeneously, adopt discharge plasma sintering molding, sintering process parameter is: sintering temperature 1000～1300 DEG C, sintering time 5～15min, pressure 30～60MPa.
3. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 2, described high-entropy alloy-base composite material includes following component, by volume percentage ratio composition:
High-entropy alloy powder 55～95%,
Titanium diboride 5%～45%.
4. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 3, described high-entropy alloy powder includes following component, by mole composition:
Aluminum 15～25%,
Ferrum 15～25%,
Chromium 15～25%,
Cobalt 15～25%,
Nickel 15～25%.
5. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 4, described high-entropy alloy powder also includes following component, by mole composition:
Copper 0～10%, titanium 0～10%.
6. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 2, it is characterised in that: in the first step, in high-entropy alloy matrix component, each component is with the form dispensing of its metallic element block materials.
7. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 2, it is characterised in that: in the first step, adopt intermediate frequency furnace to heat to fusion temperature 1600～2000 DEG C；Being atomized using noble gas as atomization gas, gas flow is 80～200L/s, and rate of cooling is 104K/s～106K/s, prepares high-entropy alloy powder, and high-entropy alloy powder particle mean size is 50～1 microns；Noble gas is selected from nitrogen or argon, and atomization pressure is 3～6MPa.
8. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 2, it is characterised in that: in second step, strengthening is titanium diboride mutually, and granularity is 10～1 microns.
9. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 2, it is characterised in that: in second step, strengthen phase powder and adopt V-type batch mixer or ball mill to mix homogeneously with high-entropy alloy powder.
10. the preparation method of a kind of powder metallurgy high-entropy alloy-base composite material according to claim 3-9 any one, it is characterized in that: the comprcssive strength of the high-entropy alloy-base composite material of preparation reaches at 2250～2850MPa, yield strength reaches at 1500～2315MPa, and consistency is at 99%-99.8%.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050044988A1 (en) * | 2003-09-03 | 2005-03-03 | Apex Advanced Technologies, Llc | Composition for powder metallurgy |
| CN101215663A (en) * | 2008-01-04 | 2008-07-09 | 哈尔滨工业大学 | High-entropy alloy-base composite material and preparation method thereof |
| CN103056352A (en) * | 2012-12-04 | 2013-04-24 | 中国人民解放军装甲兵工程学院 | High-entropy alloy powder material for supersonic spraying and manufacturing method thereof |
| CN105154702A (en) * | 2015-10-20 | 2015-12-16 | 北京理工大学 | Aluminum-based amorphous/high-entropy alloy composite and preparation method thereof |
-
2016
- 2016-03-04 CN CN201610124883.6A patent/CN105734324A/en active Pending
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20050044988A1 (en) * | 2003-09-03 | 2005-03-03 | Apex Advanced Technologies, Llc | Composition for powder metallurgy |
| CN101215663A (en) * | 2008-01-04 | 2008-07-09 | 哈尔滨工业大学 | High-entropy alloy-base composite material and preparation method thereof |
| CN103056352A (en) * | 2012-12-04 | 2013-04-24 | 中国人民解放军装甲兵工程学院 | High-entropy alloy powder material for supersonic spraying and manufacturing method thereof |
| CN105154702A (en) * | 2015-10-20 | 2015-12-16 | 北京理工大学 | Aluminum-based amorphous/high-entropy alloy composite and preparation method thereof |
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