CN109694971A - A kind of powder metallurgy titanium-aluminium matrix composites and preparation method thereof - Google Patents
A kind of powder metallurgy titanium-aluminium matrix composites and preparation method thereof Download PDFInfo
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- CN109694971A CN109694971A CN201910068972.7A CN201910068972A CN109694971A CN 109694971 A CN109694971 A CN 109694971A CN 201910068972 A CN201910068972 A CN 201910068972A CN 109694971 A CN109694971 A CN 109694971A
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- 239000002131 composite material Substances 0.000 title claims abstract description 50
- 239000011159 matrix material Substances 0.000 title claims abstract description 40
- UQZIWOQVLUASCR-UHFFFAOYSA-N alumane;titanium Chemical compound [AlH3].[Ti] UQZIWOQVLUASCR-UHFFFAOYSA-N 0.000 title claims abstract description 39
- 238000002360 preparation method Methods 0.000 title claims abstract description 33
- 238000004663 powder metallurgy Methods 0.000 title claims abstract description 20
- 239000000843 powder Substances 0.000 claims abstract description 77
- 238000005275 alloying Methods 0.000 claims abstract description 22
- ZKATWMILCYLAPD-UHFFFAOYSA-N niobium pentoxide Inorganic materials O=[Nb](=O)O[Nb](=O)=O ZKATWMILCYLAPD-UHFFFAOYSA-N 0.000 claims abstract description 11
- 238000000713 high-energy ball milling Methods 0.000 claims abstract description 10
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 claims abstract description 4
- 238000000498 ball milling Methods 0.000 claims description 25
- 238000005245 sintering Methods 0.000 claims description 24
- 239000010936 titanium Substances 0.000 claims description 18
- 229910000831 Steel Inorganic materials 0.000 claims description 10
- 239000010959 steel Substances 0.000 claims description 10
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical group CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 claims description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 9
- 229960000935 dehydrated alcohol Drugs 0.000 claims description 9
- 238000001035 drying Methods 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 9
- 238000010438 heat treatment Methods 0.000 claims description 7
- 238000010792 warming Methods 0.000 claims description 7
- 239000004615 ingredient Substances 0.000 claims description 2
- 239000000463 material Substances 0.000 abstract description 21
- 239000002994 raw material Substances 0.000 abstract description 4
- 238000005452 bending Methods 0.000 abstract description 2
- 239000011246 composite particle Substances 0.000 abstract description 2
- 230000006835 compression Effects 0.000 abstract description 2
- 238000007906 compression Methods 0.000 abstract description 2
- 239000002245 particle Substances 0.000 description 15
- 238000000034 method Methods 0.000 description 14
- 239000004411 aluminium Substances 0.000 description 6
- 229910052782 aluminium Inorganic materials 0.000 description 6
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 6
- 239000013078 crystal Substances 0.000 description 6
- 238000000227 grinding Methods 0.000 description 6
- 239000000956 alloy Substances 0.000 description 5
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 description 5
- 229910052593 corundum Inorganic materials 0.000 description 5
- 238000009826 distribution Methods 0.000 description 5
- 238000011065 in-situ storage Methods 0.000 description 5
- OGIDPMRJRNCKJF-UHFFFAOYSA-N titanium oxide Inorganic materials [Ti]=O OGIDPMRJRNCKJF-UHFFFAOYSA-N 0.000 description 5
- 229910001845 yogo sapphire Inorganic materials 0.000 description 5
- 229910010038 TiAl Inorganic materials 0.000 description 4
- 229910045601 alloy Inorganic materials 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 239000011812 mixed powder Substances 0.000 description 4
- 229910000838 Al alloy Inorganic materials 0.000 description 3
- 238000005266 casting Methods 0.000 description 3
- 238000004519 manufacturing process Methods 0.000 description 3
- 238000003701 mechanical milling Methods 0.000 description 3
- 238000004321 preservation Methods 0.000 description 3
- 230000008569 process Effects 0.000 description 3
- 238000005204 segregation Methods 0.000 description 3
- 238000002791 soaking Methods 0.000 description 3
- 238000009833 condensation Methods 0.000 description 2
- 230000005494 condensation Effects 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229910006281 γ-TiAl Inorganic materials 0.000 description 2
- 241001085205 Prenanthella exigua Species 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000003026 anti-oxygenic effect Effects 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000003631 expected effect Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 230000003116 impacting effect Effects 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 238000011031 large-scale manufacturing process Methods 0.000 description 1
- 238000005259 measurement Methods 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000007709 nanocrystallization Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000000047 product Substances 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000002002 slurry Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 238000012360 testing method Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- 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
-
- 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
-
- 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
- C22C32/001—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 only oxides
- C22C32/0015—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 only oxides with only single oxides as main non-metallic constituents
- C22C32/0036—Matrix based on Al, Mg, Be or alloys thereof
-
- 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
-
- 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
- B22F2998/00—Supplementary information concerning processes or compositions relating to powder metallurgy
- B22F2998/10—Processes characterised by the sequence of their steps
Abstract
The invention discloses a kind of powder metallurgy titanium-aluminium matrix composites and preparation method thereof, which includes the element powders component of following weight percent: Ti powder 30.0 ~ 40.0%, TiO2Powder 2.0 ~ 8.0%, Nb2O5Powder 1.0 ~ 5.0%, surplus are Al powder.The present invention can be realized as the alloying between alloying element using element powders as raw material, by high-energy ball milling, and titanium-aluminium matrix composites are made, and preparation method is simple to operation, and preparation process flow is simple, and equipment operation is easy, and raw material are cheap and easy to get.Obtained microstructure of composite particle is tiny, it can reach nanoscale, it is evenly distributed, with higher bending strength, compression strength, hardness and boundary strength, and then improve its stability and wearability, performance more excellent titanium-aluminium matrix composites can be obtained in the case where low in cost by realizing, and had in high-temperature structural material field and be applied even more extensively.
Description
Technical field
The present invention relates to the preparation method of titanium-aluminium matrix composites more particularly to a kind of powder metallurgy titanium-aluminium matrix composites
And preparation method thereof, belong to high-temperature structural material processing technique field.
Background technique
Currently, with the high speed development of China's industry, there are an increasingly higher demands to the application aspect of material, and titanium aluminium
Based alloy possesses high-melting-point, low-density, high specific strength, high ratio modulus as a kind of emerging metallic compound structural material
Etc. a series of feature, in addition to this, sufficiently high strength and stiffness can still be maintained at high temperature, and have good
The outstanding features such as creep resistant and antioxygenic property.This becomes most potential applied to the high-temperature technologies such as Aeronautics and Astronautics field
High-temperature structural material.
Titanium-aluminium matrix composites are prepared by traditional casting method mostly, and titanium valve and aluminium powder are melted it
Directly carry out Alloying Treatment afterwards, and thus obtained as-cast structure is usually that coarse branch is crystalline, there are shrinkage cavity it is loose and
Component segregation causes its brittleness to increase, and room-temperature ductility is very low to will affect performance to which formability is very poor in use,
It reduces the service life, in addition to this, the cost that traditional casting method is spent is very high, and productivity effect is low, and application is not extensive.Cause
This needs to find a kind of preparation method that can replace casting, and the titanium aluminum-base composite of more excellent performance is obtained under lower cost
Material.
Powder metallurgic method can effectively reduce material gross segregation, refinement crystal grain, avoid difficult ingot formation and direct
Conventional forging or roll forming are carried out, is currently the hot spot studied both at home and abroad.As patent No. CN201210131206.9 is disclosed
A kind of preparation method of powder metallurgy Ultra-fine Grained titanium aluminium base alloy plate, takes prealloy using rotating electrode atomized legal system, passes through
Forming and sintering, are prepared titanium aluminium base alloy plate, but prealloy method (is generally atomized using pre-alloyed powder in this method
Method, rotary electrode method preparation), it is carried out using strengthened sintering technologies such as hot pressed sintering, HIP sintering, discharge plasma sinterings
Densification.The preparation the high requirements on the equipment of prealloy powder, low output, the production cost is very high.And prealloy powder granularity generally compared with
Slightly (30~200m), pattern are spherical shape or spherical, and specific surface area is small, and sintering character is poor, so intensified-sintered work must be used
Skill could prepare the alloy material of high-compactness, and the same the high requirements on the equipment of these sintering methods, at high cost, limit it and answer
Use range.
Summary of the invention
In view of the above shortcomings of the prior art, the purpose of the present invention is to provide a kind of powder metallurgy titanium-aluminium matrix composites
And preparation method thereof, solve existing preparation method there are at high cost, complex process, equipment requirement is high and performance is bad the problems such as.
In order to solve the above-mentioned technical problem, present invention employs the following technical solutions: a kind of powder metallurgy titanium aluminium base is multiple
Condensation material, the element powders component including following weight percent: Ti powder 30.0 ~ 40.0%, TiO2Powder 2.0 ~ 8.0%, Nb2O5
Powder 1.0 ~ 5.0%, surplus are Al powder.Select the proportion that element powders can directly be made to carry out alloying shape by high-energy ball milling
At γ-TiAl matrix, and fabricated in situ mass fraction be about 10% ~ 15% Dispersed precipitate the second phase Al2O3Particle is not necessarily to
Second Phase Particle is added by the external world, the interface between composite material would not be also polluted, improve the combination of composite material interface
Intensity.The the second phase Al generated2O3Particle can thinning TiAl tissue particles, while Nb2O5Particle is added to composite material increasing
Certain room-temperature ductility is added.
The preparation method of above-mentioned powder metallurgy titanium-aluminium matrix composites, comprising the following steps:
1) ingredient is carried out by element powders component, then puts it into vacuum ball mill, then add steel ball and ball-milling medium is laggard
Row high-energy ball milling makes the element powders complete alloying；
2) by the powder of ball milling alloying after drying, discharge plasma sintering to get arrive the powder metallurgy titanium aluminum-base composite
Material.
The present invention uses discharge plasma sintering (SPS), which is to promote material using Impulsive Current effect
The features such as solidification of material has heating rate fast, and sintering temperature is low, can effectively reduce the sintering temperature of TiAl alloy, and try
Sample is short in hot stage soaking time, can effectively reduce the reduction of the material density as caused by Kinkendal Effect.This another hair
Bright middle Nb constituent content is smaller (being no more than 5%), and segregation will not impact structure property.
Preferably, the steel ball and the mass ratio of element powders total amount are 3 ~ 5:1.
Preferably, the ball-milling medium is dehydrated alcohol, and the drum's speed of rotation is 250 ~ 500r/min.Dehydrated alcohol is made
For ball-milling medium, can to avoid in mechanical milling process materials from bonding improve grinding efficiency on steel ball, and dehydrated alcohol is easily waved
Hair, is conducive to slurry not oxidized drying at low temperature after ball milling.
Preferably, the ball-milling medium and the mass ratio of element powders total amount are 3 ~ 5:1, and Ball-milling Time is 2 ~ 6h.It is preferred that
, the mass ratio of ball-milling medium and element powders total amount is 3:1, Ball-milling Time 6h.
Ratio of grinding media to material is the quality of abrading-ball (ball-milling medium) and the mass ratio of material (element powders total amount), if ratio of grinding media to material
Too small, milling intensity is not achieved, and the impact in mechanical milling process grinds effect and do not reach requirement；If ratio of grinding media to material is too big, between abrading-ball,
Impact and friction between abrading-ball and ball grinder increase, and will cause idle work loss, this not only increases power consumption when ball milling, produce
Amount reduces, and can aggravate the abrasion of ball grinder, increases metal consumption, and the metal of consumption will be also introduced into material as impurity,
From the point of view of identical Ball-milling Time, ratio of grinding media to material is that 3:1 has reached requirement.
Ball-milling Time will affect the degree of refinement of alloying and particle, and in mechanical milling process, powder is new because rubbing, impacting
Surface is constantly exposed, and makes powder generation serious the defects of deforming and foring highdensity dislocation, improves member
The free energy of element, it is final to realize nano-crystallization and alloying.Ball-milling Time is too long or too short expected effect is all not achieved.
Preferably, the drying temperature is 40 ~ 60 DEG C, dry 25 ~ 40h.
Preferably, the discharge plasma sintering is under conditions of pressure is 40 MPa, with the liter of 80 ~ 100 DEG C/min
Warm rate is warming up to 1000 ~ 1250 DEG C, keeps the temperature 10min ~ 30min, is then cooled to room temperature with 300 DEG C/min.
The consistency of sintering pressure and tissue of sintered body has a great impact, and sintering pressure is excessively high so that particle is deformed
Or it is broken, and the requirement to equipment is higher；And sintering pressure is too low that green density can be made inadequate, the densification of sintered body is difficult to
It completes, causes there are hole between particle, agglomerate is not easily molded.Therefore the present invention has selected an equipment to be able to satisfy and can be complete
The sintering pressure 40MPa densified at sintered body.Sintering temperature is excessively high or soaking time is too long can all make coarse grains, reduce multiple
The mechanical property of condensation material；Sintering temperature is too low or soaking time is too short can prevent internal stress caused by sintering process from sufficiently releasing
It puts；And the Composite Sintering block of the tiny function admirable of crystal grain can be obtained under sintering condition of the invention.SPS sintering process
Middle rate of temperature fall is 300 DEG C/min, and quickly cooling can be very good growing up for control crystal grain, improves the mechanical property of composite material
Energy.
Compared with prior art, the invention has the following beneficial effects:
1, the present invention can be realized as the alloying between alloying element by high-energy ball milling using element powders as raw material, be made
Titanium-aluminium matrix composites, preparation method of the present invention is simple to operation, and preparation process flow is simple, with short production cycle, equipment operation
Simplicity, raw material are cheap and easy to get, greatly reduce production cost, are conducive to industrialization large-scale production, solve prealloy method
There is a problem of that at high cost and equipment requirement is high, has a good application prospect and economic benefit.
2, in the titanium-aluminium matrix composites that the present invention is prepared, the second phase Al of fabricated in situ Dispersed precipitate2O3Particle with
Netted mode is distributed on matrix TiAl crystal boundary, Al2O3Titanium-aluminium alloy tissue can be refined as reinforced phase, and fabricated in situ
Al2O3The compatibility of particle and matrix is good, will not pollute the interface between composite material, make the bond strength of composite material interface
It is improved, thus obtained microstructure of composite particle is tiny, can reach nanoscale, and distribution is also more uniform, so
Compared with common titanium-aluminium matrix composites, titanium-aluminium matrix composites prepared by the present invention have higher bending strength, resist
Compressive Strength, hardness and boundary strength, and then its stability and wearability are improved, realizing can in the case where low in cost
The more excellent titanium-aluminium matrix composites of performance are obtained, has in high-temperature structural material field and is applied even more extensively.
Detailed description of the invention
Fig. 1 is the micro-organization chart of titanium-aluminium matrix composites prepared by embodiment 1.
Specific embodiment
Below with reference to embodiment, the present invention is described in further detail.
One, a kind of preparation method of powder metallurgy titanium-aluminium matrix composites
Embodiment 1
It is respectively the 24.0g Ti powder of 300 mesh, 30.0g Al powder, 4.8g TiO by granularity2Powder, 3.0g Nb2O5Powder is packed into true
In empty ball mill, adds 180g steel ball and 60g dehydrated alcohol carries out high-energy ball milling, powder after revolving speed 250r/min, ball milling 2h
Complete alloying in end；Then the powder of alloying is dried in vacuo 30h at 50 DEG C, then under conditions of pressure is 40 MPa,
Mixed-powder after above-mentioned drying is put into SPS equipment and is sintered, is warming up to 1000 DEG C with the heating rate of 100 DEG C/min, and
Room temperature is cooled to 300 DEG C/min after heat preservation 10min, finally obtains titanium-aluminium matrix composites.Examination is made in the composite material again
After sample, pre- sample preparation is obtained.
The titanium-aluminium matrix composites that the present embodiment obtains are observed under a scanning electron microscope, as a result as shown in Figure 1.
It can be seen from the figure that burning tissue mainly with grey γ-TiAl mutually for matrix, the black along crystal boundary distribution is mutually
Al2O3Particle, greyish white part are α2-Ti3The Al of a small amount of bright white is also distributed in grain boundaries in Al phase3Nb particle.Fabricated in situ
Reinforced phase Al2O3It is distributed on matrix TiAl crystal boundary in netted mode, compared with common titanium-aluminium matrix composites, is had more
Good boundary strength, stability and high-temperature behavior.
Embodiment 2
It is respectively the 18.0g Ti powder of 300 mesh, 40.0g Al powder, 1.2g TiO by granularity2Powder, 0.6g Nb2O5Powder is packed into true
In empty ball mill, adds 300g steel ball and 60g dehydrated alcohol carries out high-energy ball milling, powder completes alloying after ball milling 2h；So
The powder of alloying is dried in vacuo 25h at 60 DEG C afterwards, then under conditions of pressure is 40 MPa, it will be mixed after above-mentioned drying
It closes powder to be put into SPS equipment and is sintered, is warming up to 1000 DEG C with the heating rate of 100 DEG C/min, and keep the temperature after 10min with 300
DEG C/min is cooled to room temperature, finally obtain titanium-aluminium matrix composites.After sample is made in the composite material again, pre- sample preparation is obtained.
Embodiment 3
It is respectively 300 mesh 23.0g Ti powder, 33.0g Al powder, 3.5g TiO by granularity2Powder, 0.8g Nb2O5Powder be packed into it is true
In empty ball mill, adds 420g steel ball and 60g dehydrated alcohol carries out high-energy ball milling, powder after revolving speed 250r/min, ball milling 2h
Complete alloying in end；Then the powder of alloying is dried in vacuo 30h at 50 DEG C, then under conditions of pressure is 40 MPa,
Mixed-powder after above-mentioned drying is put into SPS equipment and is sintered, is warming up to 1000 DEG C with the heating rate of 100 DEG C/min, and
Room temperature is cooled to 300 DEG C/min after heat preservation 10min, finally obtains titanium-aluminium matrix composites.Examination is made in the composite material again
After sample, pre- sample preparation is obtained.
Embodiment 4
It is respectively the 20.0g Ti powder of 300 mesh, 37.0g Al powder, 2.0g TiO by granularity2Powder, 1.0g Nb2O5Powder be packed into
It in vacuum ball mill, adds 180g steel ball and 60g dehydrated alcohol and carries out high-energy ball milling, after revolving speed 250r/min, ball milling 2h
Powder completes alloying；Then the powder of alloying is dried in vacuo 40h at 40 DEG C, then in the condition that pressure is 40 MPa
Under, the mixed-powder after above-mentioned drying is put into SPS equipment and is sintered, is warming up to 1250 DEG C with the heating rate of 80 DEG C/min,
And keep the temperature and room temperature is cooled to 300 DEG C/min after 10min, finally obtain titanium-aluminium matrix composites.The composite material is made again
After sample, pre- sample preparation is obtained.
Embodiment 5
It is respectively the 20.0g Ti powder of 300 mesh, 36.0g Al powder, 1.8g TiO by granularity2Powder, 0.8g Nb2O5Powder is packed into true
In empty ball mill, adds 180g steel ball and 60g dehydrated alcohol carries out high-energy ball milling, powder after revolving speed 250r/min, ball milling 6h
Complete alloying in end；Then the powder of alloying is dried in vacuo 30h at 50 DEG C, then under conditions of pressure is 40 MPa,
Mixed-powder after above-mentioned drying is put into SPS equipment and is sintered, is warming up to 1000 DEG C with the heating rate of 100 DEG C/min, and
Room temperature is cooled to 300 DEG C/min after heat preservation 10min, finally obtains titanium-aluminium matrix composites.Examination is made in the composite material again
After sample, pre- sample preparation is obtained.
Two, product testing
1, tissue signature's measurement is carried out to titanium aluminium powder prepared by embodiment 1 ~ 5, the results are shown in Table 1.
Table 1
| Pre- sample preparation | Particle mean size (μm) | Distribution consistency degree |
| Embodiment 1 | 21.8 | 0.58 |
| Embodiment 2 | 20.5 | 0.52 |
| Embodiment 3 | 19.1 | 0.50 |
| Embodiment 4 | 22 | 0.60 |
| Embodiment 5 | 20.8 | 0.72 |
As it can be seen from table 1 the titanium aluminum-based powder particle fine uniform of preparation of the invention, and amount of powder particle size is reachable
To nanoscale；And in scope of embodiments, ratio of grinding media to material is bigger, and the distribution consistency degree of obtained titanium-aluminium matrix composites is smaller, grain
Diameter variation range is bigger；Ball-milling Time is longer, and the distribution consistency degree of mechanical alloying powder is higher.
2, the mechanical performance of pre- sample preparation made from the titanium-aluminium matrix composites to embodiment 1 ~ 5 is measured, as a result such as table 2
It is shown.
Table 2
| Pre- sample preparation | Room temperature compression performance/MPa | Hardness HV/ MPa |
| Embodiment 1 | 1459 | 490.4 |
| Embodiment 2 | 1463 | 475.1 |
| Embodiment 3 | 1456 | 487.9 |
| Embodiment 4 | 1433 | 480.6 |
| Embodiment 5 | 1449 | 489.7 |
From table 2 it can be seen that the pre- sample preparation prepared under suitable ball milling parameter room temperature compressibility with higher and hardness number,
And then the hardness and wearability of titanium-aluminium alloy are improved, this is mainly due to the Al by growth in situ2O3It can be thin as reinforced phase
Change titanium-aluminium alloy tissue, improves its mechanical performance.
The foregoing is merely illustrative of the preferred embodiments of the present invention, is not limitation with the present invention, all in essence of the invention
Made any modifications, equivalent replacements, and improvements etc., should all be included in the protection scope of the present invention within mind and principle.
Claims (9)
1. a kind of powder metallurgy titanium-aluminium matrix composites, which is characterized in that the element powders component including following weight percent:
Ti powder 30.0 ~ 40.0%, TiO2Powder 2.0 ~ 8.0%, Nb2O5Powder 1.0 ~ 5.0%, surplus are Al powder.
2. powder metallurgy titanium-aluminium matrix composites according to claim 1, which is characterized in that including following weight percent
Element powders component: Ti powder 35.0 ~ 38.0%, TiO2Powder 2.0 ~ 6.0%, Nb2O5Powder 1.0 ~ 5.0%, surplus are Al powder.
3. powder metallurgy titanium-aluminium matrix composites according to claim 1 or claim 2, which is characterized in that the grain of the element powders
Degree is 100 mesh ~ 300 mesh.
4. the preparation method of powder metallurgy titanium-aluminium matrix composites as claimed in claim 1 or 2, which is characterized in that including following
Step:
1) ingredient is carried out by element powders component as claimed in claim 1 or 2, then puts it into vacuum ball mill, then add steel
High-energy ball milling is carried out after ball and ball-milling medium, and the element powders is made to complete alloying；
2) by the powder of ball milling alloying after drying, discharge plasma sintering to get arrive the powder metallurgy titanium aluminum-base composite
Material.
5. the preparation method of powder metallurgy titanium-aluminium matrix composites according to claim 4, which is characterized in that the steel ball with
The mass ratio of element powders total amount is 3 ~ 7:1.
6. the preparation method of powder metallurgy titanium-aluminium matrix composites according to claim 4, which is characterized in that the ball milling is situated between
Matter is dehydrated alcohol.
7. the preparation method of powder metallurgy titanium-aluminium matrix composites according to claim 4, which is characterized in that the ball mill
Revolving speed is 250r/min, and the Ball-milling Time is 2 ~ 6h.
8. the preparation method of powder metallurgy titanium-aluminium matrix composites according to claim 4, which is characterized in that described electric discharge etc.
Ion sintering is to be warming up to 1000 ~ 1250 DEG C under conditions of pressure is 40 MPa with the heating rate of 80 ~ 100 DEG C/min, protect
Then warm 10min ~ 30min is cooled to room temperature with 300 DEG C/min.
9. the preparation method of powder metallurgy titanium-aluminium matrix composites according to claim 4, which is characterized in that the dry temperature
40 ~ 60 DEG C of degree, dry 25 ~ 40h.
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