CN103343251A - Sintering Ti-Al-based alloy porous material, application thereof and method for improving pore structure of sintering Ti-Al-based alloy porous material - Google Patents
Sintering Ti-Al-based alloy porous material, application thereof and method for improving pore structure of sintering Ti-Al-based alloy porous material Download PDFInfo
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Abstract
The invention discloses a sintering Ti-Al-based alloy porous material capable of improving corrosion resistance, a filtering element applying the material, and a method for improving the pore structure of the material. The sintering Ti-Al-based alloy porous material has the following characteristics: a) the material mainly comprises three elements of Ti, Al and C, and the total weight of the three elements accounts for over 90 percent of the weight of the sintering material, wherein Ti is 50 to 85 percent of the total weight of Ti and Al, and C is 0.5 to 15 percent of the total weight of Ti and Al; b) the C of the material mainly exists in at least one form of a carbon solid solution of a Ti-Al-based compound and carbide of a Ti-Al-based compound, or mainly exists in the forms of carbide of the Ti-Al-based compound and TiC, and is uniformly distributed in the sintering Ti-Al-based alloy porous material roughly; c) the porosity is 30 to 60 percent; the average aperture is 0.5 to 50 microns; the tensile strength is more than or equal to 30 MPa; the pure water filtration flux of the sintering Ti-Al-based alloy porous material with the thickness being less than or equal to 5 mm is more than or equal to 1 t/m2.h at 0.05Mpa filter pressure difference; the weight loss ratio is below 0.8 percent after the sintering Ti-Al-based alloy porous material is soaked in 5 wt% hydrochloric acid solution at room temperature for 8 days.
Description
Technical field
The present invention relates to a kind of porous material and use the filtering element of this porous material, be specifically related to a kind of sintering Ti-Al base alloy porous material by the powder metallurgic method preparation and use the filtering element of this porous material.The invention still further relates to the method for improving sintering Ti-Al base alloy porous material hole structure.
Background technology
At present the research of sintered porous material is mainly concentrated on the discussion of optimization of preparation, pore-forming mechanism, the improvement of material property and the several aspects of expansion of range of application.Wherein, with regard to pore-forming mechanism, the pore-forming mode that has been applied among the sintered porous material preparation method mainly contains: first, by the chemical reaction pore-forming, its principle is based on the caused inclined to one side diffusional effect of larger difference of different element intrinsic diffusion coefficients, makes to produce the Kirkendall hole in the material; The second, pile up pore-forming by the raw material particle physics; The 3rd, deviate from pore-forming by added ingredients.The selection of above-mentioned several pore-forming modes and combination inevitably can cause direct influence to the pore structure of porous material.And the pore structure of porous material can further determine the performance of porous material.Therefore, the sintered porous material that generates based on different pore-forming modes often has pore structure and the use properties of differentiation, by understanding and the measurement to them, can make these porous materials clearerly to be identified and to characterize.At present, in order to characterize porous material fully, adopt usually this area: 1) material composition and content; 2) pore structure mainly comprises porosity, aperture etc.; 3) material property parameter comprises penetrating quality, mechanical strength and chemical stability, and wherein, penetrating quality fluid permeability method commonly used is measured, and mechanical strength represents with tensile strength that usually chemical stability is mainly with acidproof and/or alkaline can the expression.
The Ti-Al intermetallic compound porous material is a kind of sintering inorganic porous material between superalloy and pottery.Because it according to metallic bond and the common combination of covalent linkage, has the common advantage of metallic substance and stupalith concurrently, therefore, the Ti-Al intermetallic compound porous material has broad application prospects as filtering material.Have excellent performance although the Ti-Al intermetallic compound porous material is generally acknowledged, its corrosion resistance nature under strong acid condition still has much room for improvement.Such as, Al content be the Ti-Al intermetallic compound porous material of 35wt% under 90 ℃ constant temperature, when the pH value dropped to 2 from 3, the mass loss of sample and open porosity and all enlarge markedly showed that the corrosion resistance nature of material descends more obvious.Therefore, at some special application scenarios, also need further to improve the erosion resistance of material.Before the application's the applying date, also do not find a kind of erosion resistance that can either improve the Ti-Al intermetallic compound porous material, can attach again simultaneously and improve the material hole structure, and reach the sintering Ti-Al base alloy porous material of good comprehensive use properties.
Summary of the invention
The application's technical problem to be solved provides a kind of sintering Ti-Al base alloy porous material of erosion resistance and filtering element of using this porous material of improving.The application also will provide a kind of method of improving sintering Ti-Al base alloy porous material hole structure in addition.
The application's sintering Ti-Al base alloy porous material has following feature:
A) it is mainly elementary composition by Ti, Al, three kinds of C, and the weight sum of these three kinds of elements accounts for more than 90% of this sintering Ti-Al base alloy porous material weight, and wherein, Ti is 50～85% of Ti, Al gross weight, and C is 0.5～15% of Ti, Al gross weight;
B) C in this sintering Ti-Al base alloy porous material exists with at least a form in the carbide of the carbon sosoloid of Ti-Al based compound and Ti-Al based compound, or mainly exist with the carbide of Ti-Al based compound and the form of TiC, and in this sintering Ti-Al base alloy porous material, evenly distribute haply;
C) its porosity is 30～60%, and mean pore size is 0.5～50 μ m, tensile strength 〉=30MPa, the filtration flux 〉=1t/m of sintering Ti-Al base alloy porous material pure water under the filtration pressure difference of 0.05MPa of thickness≤5mm
2H, the rate of weight loss of soaking at room temperature after 8 days is below 0.8% in the hydrochloric acid soln of 5wt%.
Above-mentioned sintering Ti-Al base alloy porous material is can be only elementary composition by Ti, Al, three kinds of C, also can in the scope that is no more than sintering Ti-Al base alloy porous material gross weight 10%, add other materials except Ti, Al, C, for example one or more elements among Cr, Mo, V, Nb, Si, the W.Suggestion at present controls the weight sum of Ti, Al, three kinds of elements of C in this porous material at more than 95%, 97%, 98% or 99% of porous material weight, thereby can either guarantee the performance of sintering Ti-Al base alloy porous material, simultaneously also can simplify raw material type, be convenient to produce.
When sintering Ti-Al base alloy porous material was elementary composition by three kinds of Ti, Al, C, according to the variation of C content, the composition of the crystallization phases in this sintering Ti-Al base alloy porous material can comprise following several situation:
1) crystallization phases of this sintering Ti-Al base alloy porous material is made up of the Ti-Al-C ternary alloy, and C wherein is solid-solubilized in this alloy as solute;
2) crystallization phases of this sintering Ti-Al base alloy porous material is made up of compound between the Ti-Al binary metal and Ti-Al-C ternary MAX phase compound, and wherein Ti-Al-C ternary MAX phase compound is Ti
2AlC, Ti
3AlC
2In at least a;
3) crystallization phases of this sintering Ti-Al base alloy porous material is made up of Ti-Al-C ternary MAX phase compound, and wherein Ti-Al-C ternary MAX phase compound is Ti
2AlC, Ti
3AlC
2In at least a;
4) crystallization phases of this sintering Ti-Al base alloy porous material is made up of Ti-Al-C ternary MAX phase compound and TiC, and wherein Ti-Al-C ternary MAX phase compound is Ti
2AlC, Ti
3AlC
2In at least a.
The filtering element that the application provides, this filtering element contain above-mentioned sintering Ti-Al base alloy porous material.
The application's sintering Ti-Al base alloy porous material has following beneficial technical effects:
One, has advantages of higher tensile strength and excellent corrosion resistance nature;
Two, especially surprisingly, when the carbide of the Ti-Al based compound that comes into existence in the material, owing to the C in the raw material and Ti reaction have improved pore structure, make the tortuosity of three-dimensional communicating pores diminish, reduce the resistance that passes through of filtration medium, can obtain more preferably filtration flux;
Three, formed by Ti-Al-C ternary MAX phase compound substantially when the crystallization phases of sintering Ti-Al base alloy porous material, and this Ti-Al-C ternary MAX phase compound is specially Ti
3AlC
2The time, the corrosion resistance nature of material is better.
The application improves the method for sintering Ti-Al base alloy porous material hole structure, is to contain Ti powder and TiH
2Thereby the mixed powder of at least a, the Al powder in the powder and C powder carries out granulation, drying, moulding and sintering successively prepares a kind of sintering Ti-Al base alloy porous material, wherein, during sintering Ti both with Al reaction pore-creating, react with C again.In this method, the C in the raw material and Ti react and have improved pore structure, make the tortuosity of three-dimensional communicating pores diminish, and have reduced the resistance that passes through of filtration medium, can obtain more preferably filtration flux.
Embodiment
Be specifically described to the preparation method of sintering Ti-Al base alloy porous material with by the sintering Ti-Al base alloy porous material that these methods obtain below by experiment.By these explanations, those skilled in the art can know the outstanding feature that the basic alloy porous material of the sintering Ti-Al that recognizes the application has.The numbering of the experimental example that below relates to is consistent with the numbering of corresponding " pressed compact ", " sample ".
For explanation the application's sintering Ti-Al base alloy porous material and preparation thereof, following 12 groups of experimental examples have been prepared altogether.Wherein, the sample 1 to 7 for preparing respectively of example 1 to 7 all belongs within the scope of the claimed sintering Ti-Al base of the application's claim 1 alloy porous material by experiment.Experimental example 8 to 12 all uses " * " to mark as the contrast experiment who embodies experimental example 1 to 7 substantive distinguishing features and technique effect on its numbering, in order to distinguish.Experimental example 8 specifically is the content that has increased Ti powder and C powder in the raw material on the basis of experimental example 3, and the sample 8 that will prepare thus compares with sample 3.Experimental example 9 specifically is on the basis of experimental example 4, changes raw material C powder raw material into TiC powder (C content is constant), and the sample 9 that will prepare thus compares with sample 4.Experimental example 10 directly uses Ti
3AlC
2Powder is that raw material prepares porous material.12 of experimental example 11 and experimental examples have been implemented a kind of existing sintering Ti-Al base alloy porous material preparation method respectively.Specific as follows.
One, material preparation process
The material composition of experimental example 1 to 12 and content (by weight percentage) see Table 1.For ease of comparing, unified employing particle diameter is-400 purpose Ti powder and TiC powder, and particle diameter is-325 purpose TiH
2Powder, particle diameter are the Al powder of 10～15 μ m, and particle diameter is that C powder, the particle diameter of 3～5 μ m is the Ti of 15～20 μ m
3AlC
2Powder and particle diameter are-100 purpose NH
4HCO
3(pore-forming material).Certainly, in actual production, those skilled in the art also can adjust the particle diameter of each raw material targetedly according to the aperture of its porous material that will obtain.
Material composition and the content thereof listed from table 1 can calculate: the Ti powder accounts for 66.66% of Ti powder, Al powder gross weight the experimental example 1, and the C powder accounts for 0.5% of Ti powder, Al powder gross weight; The Ti powder accounts for 75.52% of Ti powder, Al powder gross weight in the experimental example 2, and the C powder accounts for 8% of Ti powder, Al powder gross weight; The Ti powder accounts for 81.2% of Ti powder, Al powder gross weight in the experimental example 3, and the C powder accounts for 13.64% of Ti powder, Al powder gross weight; Experimental example 4 is very approaching with the content of experimental example 3, and the difference on its content is because Ti and TiH
2The faint difference of weight causes; The Ti powder accounts for 85% of Ti powder, Al powder gross weight in the experimental example 5, and the C powder accounts for 15% of Ti powder, Al powder gross weight; The Ti powder accounts for 81.6% of Ti powder, Al powder gross weight in the experimental example 6, and the C powder accounts for 13.64% of Ti powder, Al powder gross weight, and the Si powder accounts for 5% of raw material gross weight; The Ti powder accounts for 81.6% of Ti powder, Al powder gross weight in the experimental example 7, and the C powder accounts for 13.64% of Ti powder, Al powder gross weight, and the Cr powder accounts for 7% of raw material gross weight; The Ti powder accounts for 92.80% of Ti powder, Al powder gross weight in the experimental example 8, and the C powder accounts for 19.87% of Ti powder, Al powder gross weight.The raw material of experimental example 11 and experimental example 12 (has specifically adopted NH by pore-forming material
4HCO
3), TiH
2Powder, TiC powder, Al powder are formed; In the experimental example 11, NH
4HCO
3, TiH
2The content (atomic percent) of powder, TiC powder and Al is respectively 15%, 35%, 35%, 15%, is scaled weight percent and is respectively 21.78%, 32.17%, 38.61% and 7.44%; In the experimental example 12, NH
4HCO
3, TiH
2The content (atomic percent) of powder, TiC powder and Al is respectively 5%, 35%, 50%, 10%, be scaled weight percent be respectively 7.29%, 32.32%, 55.42% and 4.97%(see Table 1).
Table 1: composition and content that experimental example 1 to 10 is raw materials used
It is listed to press table 1, and the raw material to experimental example 1 to 12 mixes respectively.After fully mixing, consider in the raw material of experimental example 1 to 8 all to be mixed with the lighter C powder of weight, cause segregation easily, therefore, also need the powder of experimental example 1 to 8 is carried out granulation, carry out drying after the granulation again, drying temperature is set at 55 ℃, is set at 6 hours time of drying.And experimental example 9 to 12 does not contain the C powder, thereby need not to carry out granulation and can enter next step molding procedure.Because granulating and drying can't impact final structure and the performance of material in addition just for fear of segregation, so can not influence the accuracy of experiment contrast.
Afterwards, in the isostatic pressing mould of the unified specification of respectively powder of experimental example 1 to 12 being packed into, then these moulds are placed the cold isostatic compaction machine respectively, pressurize is 30 seconds under the 250MPa forming pressure, namely makes after the demoulding to be numbered 1 to 12 tubulose pressed compact.Then, these pressed compacts are respectively charged into the sintering boat, these sintering boats are placed carry out sintering in the sintering oven again, furnace cooling behind the sintering is obtained sample 1 to 12 at last again from each sintering boat.
1.1 the sintering schedule of experimental example 1 to 9
The sintering schedule of experimental example 1 to 9 can be divided into five stages, and wherein the fs is that sintering temperature is risen to 450 ℃ gradually from room temperature, and temperature rise rate is controlled at 1～25 ℃/min, and total sintering time in this stage is 30～600 minutes; Subordinate phase is that sintering temperature is risen to 620 ℃ gradually from 450 ℃, and temperature rise rate is controlled at 1～20 ℃/min, and total sintering time in this stage is 60～1000 minutes; Phase III is that sintering temperature is risen to 1000 ℃ gradually from 620 ℃, and temperature rise rate is controlled at 1～20 ℃/min, and total sintering time in this stage is 30～1000 minutes; The quadravalence section is that sintering temperature is risen to 1200 ℃ gradually from 1000 ℃, and temperature rise rate is controlled at 1～20 ℃/min, and total sintering time in this stage is 30～600 minutes; Five-stage is that sintering temperature is risen to 1400 ℃ gradually from 1200 ℃, and temperature rise rate is controlled at 1～20 ℃/min, is 60～600 minutes during the total sintering in this stage.The main purpose of above-mentioned fs is degreasing; The main purpose of subordinate phase is to facilitate Ti and Al reaction pore-creating to generate between the Ti-Al binary metal compound, and (in experimental example 4 and 9, this stage also has TiH concurrently
2The purpose of dehydrogenation pore-creating); The main purpose of phase III is to facilitate Ti and C reaction pore-creating to generate except the TiC(experimental example 9), further facilitate Ti and Al reaction simultaneously; The main purpose of quadravalence section is facilitated compound and TiC reaction generation Ti between the Ti-Al binary metal
2The AlC intermediate phase; The main purpose of five-stage is to facilitate Ti
2The final Ti that generates of AlC intermediate phase and TiC reaction
3AlC
2Ternary MAX phase compound.The sintering process parameter in five stages is specifically as shown in table 2 in the sintering process of experimental example 1 to 9.The unit of temperature rise rate is ℃/min in the table 2, and the unit of sintering time is minute.
Table 2: the sintering schedule of experimental example 1 to 8
1.2 the sintering schedule of experimental example 10 to 12
The sintering schedule of experimental example 10 is relatively simple, and it specifically is that sintering temperature is risen to 1400 ℃ gradually from room temperature, and temperature rise rate is controlled at 15 ℃/min, and total sintering time is 180 minutes.
The sintering schedule of experimental example 11 is divided into four-stage, and wherein the fs is that sintering temperature is risen to 150 ℃ gradually from room temperature, and temperature rise rate is controlled at 3 ℃/min, is incubated 30 minutes then, finishes NH
4HCO
3Decomposition pore-creating; Subordinate phase is that sintering temperature is risen to 480 ℃ gradually from 150 ℃, and temperature rise rate is controlled at 8 ℃/min, is incubated 120 minutes then, finishes TiH
2Dehydrogenation pore-creating; Phase III is that sintering temperature is risen to 620 ℃ gradually from 480 ℃, and temperature rise rate is controlled at 2 ℃/min, is incubated 240 minutes then, finishes the reaction pore-creating of Ti and Al, generates compound between the Ti-Al binary metal; The quadravalence section is that sintering temperature is risen to 1300 ℃ gradually from 620 ℃, and temperature rise rate is controlled at 5 ℃/min, is incubated 300 minutes then, facilitates compound and the final Ti of generation of TiC reaction between the Ti-Al binary metal
3AlC
2Ternary MAX phase compound.
The sintering schedule of experimental example 12 is divided into four-stage, and wherein the fs is that sintering temperature is risen to 350 ℃ gradually from room temperature, and temperature rise rate is controlled at 5 ℃/min, is incubated 60 minutes then, finishes NH
4HCO
3Decomposition pore-creating; Subordinate phase is that sintering temperature is risen to 560 ℃ gradually from 350 ℃, and temperature rise rate is controlled at 10 ℃/min, is incubated 60 minutes then, finishes TiH
2Dehydrogenation pore-creating; Phase III is that sintering temperature is risen to 950 ℃ gradually from 560 ℃, and temperature rise rate is controlled at 1 ℃/min, is incubated 360 minutes then, finishes the reaction pore-creating of Ti and Al, generates compound between the Ti-Al binary metal; The quadravalence section is that sintering temperature is risen to 1400 ℃ gradually from 950 ℃, and temperature rise rate is controlled at 3 ℃/min, is incubated 420 minutes then, facilitates compound and the final Ti of generation of TiC reaction between the Ti-Al binary metal
3AlC
2Ternary MAX phase compound.
Two, the phase composite of material and performance measurement thereof
For more knowing the sintering Ti-Al base alloy porous material of characterization sample 1 to 12 correspondence, below will phase composite and the material property parameter of sample 1 to 12 be described.Wherein, because experimental example 6 and 7 all is in order to study other materials of mixing except Ti, Al, C to the final Effect on Performance of material, therefore, when the illustrative material phase composite, only having selected sample 6 is example.
By XRD sample 1 to 6, sample 8 to 12 are respectively detected, its result is as shown in table 3.
Table 3: the phase composite of sample 1 to 6, sample 8 to 12
| Specimen coding | Phase composite |
| 1 | The C of TiAl, a small amount of solid solution |
| 2 | TiAl、Ti 3AlC 2 |
| 3 | Ti 3AlC 2 |
| 4 | Ti 3AlC 2 |
| 5 | Ti 3AlC 2、TiC |
| 6 | Ti 3AlC 2、TiC、Ti 3SiC 2 |
| 8＊ | Ti 3AlC 2、TiC |
| 9＊ | Ti 3AlC 2 |
| 10＊ | Ti 3AlC 2 |
| 11＊ | Ti 3AlC 2、TiC |
| 12＊ | Ti 3AlC 2、TiC |
Can draw from table 3, the phase composite of the application's sintering Ti-Al base alloy porous material is relevant with C content.Under the situation of not mixing other elements, when C content seldom the time, the crystallization phases of sintering Ti-Al base alloy porous material is made up of the Ti-Al-C ternary alloy, and C wherein is solid-solubilized in (as sample 1) in this alloy as solute; After C content increased to a certain degree, the crystallization phases of sintering Ti-Al base alloy porous material was formed (as sample 2) by compound between the Ti-Al binary metal and Ti-Al-C ternary MAX phase compound; When C content further increases, the crystallization phases of sintering Ti-Al base alloy porous material is only formed (as sample 3,4) by Ti-Al-C ternary MAX phase compound; When C content continuation increase, the crystallization phases of sintering Ti-Al base alloy porous material is formed (as sample 5) by Ti-Al-C ternary MAX phase compound with a small amount of TiC.In table 3, compound is specially the TiAl intermetallic compound between the Ti-Al binary metal, and Ti-Al-C ternary MAX phase compound is specially Ti
3AlC
2Yet along with Ti in the raw material is the decline of Ti, Al gross weight ratio, compound also can be TiAl between said Ti-Al binary metal
3Deng.In addition, known Ti-Al-C ternary MAX phase compound has Ti at present
3AlC
2And Ti
2AlC, they have similar character, therefore, by to preparation technology's control to Ti-Al-C ternary MAX phase compound also can be Ti
2AlC.
Performance test such as the table 4 of sample 1 to 12.Wherein, bubble-tube method is adopted in the test of material porosity and mean pore size, filtration flux is specially the filtration flux of pure water under the filtration pressure difference of 0.05MPa, the test of Tensile strength is to record by drawing machine after sample 1 to 12 is processed as standard test specimen by CNS GB7963-87, and it is that mass percent is 5 that the material erosion resistance adopts at 5wt%() hydrochloric acid soln in the rate of weight loss of soaking at room temperature after 8 days characterize.
Table 4: the The performance test results of sample 1 to 10
Three, test result analysis
1) referring to table 4, the tensile strength degree of sample 1 to 7 all 〉=30MPa, under the filtration pressure difference of 0.05MPa the filtration flux of pure water all 〉=1t/m
2H, the rate of weight loss of soaking at room temperature after 8 days is all at (TiAl intermetallic compound porous material then up to 2% about) below 0.8% in the hydrochloric acid soln of 5wt%.Wherein, the tensile strength of sample 1 is 32MPa, near lower value 30MPa; And from sample 2, the tensile strength of material enlarges markedly, sample 2 in 7 except sample 5, the tensile strength of all the other samples all 〉=40MPa, and the highest with the tensile strength of sample 3.The filtration flux of sample 1 is 1.1t/m
2H is equally near lower value 1.0t/m
2H; From sample 2, filtration flux significantly increases, the filtration flux of sample 2 to 7 all＞3t/m
2H.Sample 8 to 12 soaking at room temperature rate of weight loss after 8 days in the hydrochloric acid soln of 5wt% still, all incompetently in the sample 8 to 12 reaches tensile strength degree 〉=30MPa and the filtration flux 〉=1t/m of pure water under the filtration pressure difference of 0.05MPa simultaneously equally all below 0.8%
2H person.
2) about the tensile strength of material.Associative list 3, in the sample 1 to 7, along with the increase of C, compound is gradually to the transformation of Ti-Al-C ternary MAX phase compound between the Ti-Al binary metal in the material, and the tensile strength of material also is increase tendency; But along with the generation of TiC phase, the tensile strength of material produces decline (sample 5) to a certain degree.Sample 8 is than sample 3, and the content of Ti and C is higher, and the content of Al is less relatively, thus generate more TiC phase, so the tensile strength of sample 8 has been produced tangible adverse influence.The reactionless phase transformation of the sintering process of sample 10 causes the tensile strength of material also not high.Sample 11 and sample 12 all use NH
4HCO
3Make pore-forming material so obtain higher porosity, generate more TiC phase in addition, so the tensile strength of material fails to reach 30MPa equally.
3) about the perviousness of material.2 to 7 filtration flux changes from sample 1 to sample, can think: (Ti for sample 2 to 7 when the carbide of the Ti-Al based compound that comes into existence in the material
3AlC
2Phase), owing to the C in the raw material and Ti reaction has improved pore structure, makes the tortuosity of three-dimensional communicating pores diminish, reduced the resistance that passes through of filtration medium, can obtain more preferably filtration flux.Although experimental example 11 and experimental example 12 have all used pore-forming material to make the porosity of sample 11 and sample 12 meet or exceed the porosity of sample 2 to 7, the filtration flux of sample 11 and sample 12 still is starkly lower than the filtration flux of sample 2 to 7 under the essentially identical situation of mean pore size, has further proved C and Ti reaction to improving the effect of three-dimensional communicating pores tortuosity.And the Al content in the experimental example 8 to cross be to cause the not high key factor of sample 8 filtration fluxs at least.
4) in general, in order to reach than more excellent comprehensive use properties, Ti in the application's sintering Ti-Al base alloy porous material can account for Ti, Al gross weight 70%, 73%, 76%, 80% or 83%, and the C in the sintering Ti-Al base alloy porous material can account for Ti, Al gross weight 3%, 5%, 8% or 12%; Crystallization phases in the material preferably is made up of compound between the Ti-Al binary metal and Ti-Al-C ternary MAX phase compound, or directly is made up of Ti-Al-C ternary MAX phase compound; Tensile strength 〉=the 40MPa of material, under the filtration pressure difference of 0.05MPa the filtration flux of pure water all 〉=3t/m
2H.
Claims (10)
1. sintering Ti-Al base alloy porous material is characterized in that:
A) it is mainly elementary composition by Ti, Al, three kinds of C, and the weight sum of these three kinds of elements accounts for more than 90% of this sintering Ti-Al base alloy porous material weight, and wherein, Ti is 50～85% of Ti, Al gross weight, and C is 0.5～15% of Ti, Al gross weight;
B) C in this sintering Ti-Al base alloy porous material exists with at least a form in the carbide of the carbon sosoloid of Ti-Al based compound and Ti-Al based compound, or mainly exist with the carbide of Ti-Al based compound and the form of TiC, and in this sintering Ti-Al base alloy porous material, evenly distribute haply;
C) its porosity is 30～60%, and mean pore size is 0.5～50 μ m, tensile strength 〉=30MPa, the filtration flux 〉=1t/m of sintering Ti-Al base alloy porous material pure water under the filtration pressure difference of 0.05MPa of thickness≤5mm
2H, massfraction be in 5% the hydrochloric acid soln rate of weight loss of soaking at room temperature after 8 days below 0.8%.
2. sintering Ti-Al as claimed in claim 1 base alloy porous material, it is characterized in that: the weight sum of Ti, Al, three kinds of elements of C accounts for more than 95% of this sintering Ti-Al base alloy porous material weight in the described sintering Ti-Al base alloy porous material.
3. sintering Ti-Al as claimed in claim 2 base alloy porous material, it is characterized in that: described sintering Ti-Al base alloy porous material is elementary composition by Ti, Al, three kinds of C; Its crystallization phases is made up of compound between the Ti-Al binary metal and Ti-Al-C ternary MAX phase compound.
4. sintering Ti-Al as claimed in claim 2 base alloy porous material, it is characterized in that: described sintering Ti-Al base alloy porous material is elementary composition by Ti, Al, three kinds of C; Its crystallization phases is made up of Ti-Al-C ternary MAX phase compound.
5. sintering Ti-Al as claimed in claim 4 base alloy porous material, it is characterized in that: described Ti-Al-C ternary MAX phase compound is specially Ti
3AlC
2
6. sintering Ti-Al as claimed in claim 2 base alloy porous material, it is characterized in that: described sintering Ti-Al base alloy porous material is elementary composition by Ti, Al, three kinds of C; Its crystallization phases is made up of Ti-Al-C ternary MAX phase compound and TiC.
7. sintering Ti-Al as claimed in claim 1 base alloy porous material, it is characterized in that: the mean pore size of described sintering Ti-Al base alloy porous material is 1～20 μ m.
8. sintering Ti-Al as claimed in claim 1 base alloy porous material is characterized in that: also contain at least a in Cr, Mo, V, Nb, Si, the W element in the described sintering Ti-Al base alloy porous material.
9. filtering element is characterized in that: this filtering element contains the described sintering Ti-Al base of any claim alloy porous material in the claim 1 to 8.
10. improve the method for sintering Ti-Al base alloy porous material hole structure, it is characterized in that: will contain Ti powder and TiH
2Thereby the mixed powder of at least a, the Al powder in the powder and C powder carries out granulation, drying, moulding and sintering successively prepares a kind of sintering Ti-Al base alloy porous material, wherein, during sintering Ti both with Al reaction pore-creating, react with C again.
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| CN103924203A (en) * | 2014-04-24 | 2014-07-16 | 中国科学院宁波材料技术与工程研究所 | Radiation-resistant protective coating on matrix surface and preparation method thereof |
| CN104233004A (en) * | 2014-08-31 | 2014-12-24 | 成都易态科技有限公司 | Powder sintered porous filter alloy, preparation method of alloy and prepressing forming body of alloy |
| CN104291824A (en) * | 2014-09-23 | 2015-01-21 | 中国科学院金属研究所 | Method for preparing laminated conductive titanium-aluminum-carbon honeycomb ceramic by using element powder in situ and application |
| CN104404288A (en) * | 2014-11-23 | 2015-03-11 | 北京科技大学 | Method for preparing light Nb-Ti-Al based porous material |
| CN104588662A (en) * | 2014-10-31 | 2015-05-06 | 成都易态科技有限公司 | Flexible multi-hole metal foil and manufacturing method thereof |
| CN104588651A (en) * | 2014-10-31 | 2015-05-06 | 成都易态科技有限公司 | Flexible multi-hole metal foil and manufacturing method thereof |
| CN105499576A (en) * | 2016-01-11 | 2016-04-20 | 北京科技大学 | Method for preparing porous titanium-aluminium alloy through powder metallurgy |
| CN108384989A (en) * | 2018-01-25 | 2018-08-10 | 江苏大学 | Compound titanium silicon molybdenum porous material and preparation method thereof between a kind of high porosity metal |
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| CN104291824A (en) * | 2014-09-23 | 2015-01-21 | 中国科学院金属研究所 | Method for preparing laminated conductive titanium-aluminum-carbon honeycomb ceramic by using element powder in situ and application |
| CN104588662A (en) * | 2014-10-31 | 2015-05-06 | 成都易态科技有限公司 | Flexible multi-hole metal foil and manufacturing method thereof |
| CN104588651A (en) * | 2014-10-31 | 2015-05-06 | 成都易态科技有限公司 | Flexible multi-hole metal foil and manufacturing method thereof |
| CN104404288B (en) * | 2014-11-23 | 2016-08-24 | 北京科技大学 | A kind of method preparing lightweight Nb-Ti-Al based porous materials |
| CN104404288A (en) * | 2014-11-23 | 2015-03-11 | 北京科技大学 | Method for preparing light Nb-Ti-Al based porous material |
| CN105499576A (en) * | 2016-01-11 | 2016-04-20 | 北京科技大学 | Method for preparing porous titanium-aluminium alloy through powder metallurgy |
| CN105499576B (en) * | 2016-01-11 | 2018-01-16 | 北京科技大学 | A kind of method that powder metallurgy prepares porous titanium-aluminium alloy |
| CN108384989A (en) * | 2018-01-25 | 2018-08-10 | 江苏大学 | Compound titanium silicon molybdenum porous material and preparation method thereof between a kind of high porosity metal |
| CN111533558A (en) * | 2020-02-25 | 2020-08-14 | 南京明昌新材料科技有限公司 | Pure Ti3AlC2 powder, block or porous body and preparation method and application thereof |
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