CN109554567B - A kind of Ti-Fe alloy matrix composite material and preparation method thereof - Google Patents
A kind of Ti-Fe alloy matrix composite material and preparation method thereof Download PDFInfo
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- 239000002131 composite material Substances 0.000 title claims abstract description 69
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 55
- 239000000956 alloy Substances 0.000 title claims abstract description 55
- 229910011212 Ti—Fe Inorganic materials 0.000 title claims abstract description 54
- 238000002360 preparation method Methods 0.000 title claims abstract description 20
- 239000011159 matrix material Substances 0.000 title abstract description 7
- 239000000843 powder Substances 0.000 claims abstract description 44
- 239000010935 stainless steel Substances 0.000 claims abstract description 17
- 229910001220 stainless steel Inorganic materials 0.000 claims abstract description 17
- 238000003754 machining Methods 0.000 claims abstract description 9
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical class [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 23
- 239000011812 mixed powder Substances 0.000 claims description 19
- 238000002156 mixing Methods 0.000 claims description 16
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical class [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 14
- 238000001513 hot isostatic pressing Methods 0.000 claims description 13
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000001816 cooling Methods 0.000 claims description 8
- 238000003466 welding Methods 0.000 claims description 7
- 238000000034 method Methods 0.000 abstract description 20
- 238000005245 sintering Methods 0.000 abstract description 14
- 239000002245 particle Substances 0.000 abstract description 12
- 238000007872 degassing Methods 0.000 abstract description 6
- 238000004663 powder metallurgy Methods 0.000 abstract description 5
- 230000003014 reinforcing effect Effects 0.000 abstract description 5
- 239000000463 material Substances 0.000 abstract description 4
- 239000002994 raw material Substances 0.000 abstract description 4
- 238000007789 sealing Methods 0.000 abstract description 2
- 238000009827 uniform distribution Methods 0.000 abstract 1
- 239000010936 titanium Substances 0.000 description 16
- 230000006835 compression Effects 0.000 description 10
- 238000007906 compression Methods 0.000 description 10
- 239000012071 phase Substances 0.000 description 7
- 229910052719 titanium Inorganic materials 0.000 description 7
- 238000011065 in-situ storage Methods 0.000 description 5
- 229910001069 Ti alloy Inorganic materials 0.000 description 4
- 238000006243 chemical reaction Methods 0.000 description 4
- 238000011068 loading method Methods 0.000 description 4
- 238000005266 casting Methods 0.000 description 3
- 230000007547 defect Effects 0.000 description 2
- 238000000280 densification Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009849 vacuum degassing Methods 0.000 description 2
- 229910000883 Ti6Al4V Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000003153 chemical reaction reagent Substances 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 230000004927 fusion Effects 0.000 description 1
- 150000004678 hydrides Chemical class 0.000 description 1
- 239000007943 implant Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000005551 mechanical alloying Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 231100000252 nontoxic Toxicity 0.000 description 1
- 230000003000 nontoxic effect Effects 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 239000000376 reactant Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 230000002269 spontaneous effect Effects 0.000 description 1
- 238000001308 synthesis method Methods 0.000 description 1
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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
- C22C1/058—Mixtures of metal powder with non-metallic powder by reaction sintering (i.e. gasless reaction starting from a mixture of solid metal compounds)
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- 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
- B22F3/12—Both compacting and sintering
- B22F3/14—Both compacting and sintering simultaneously
- B22F3/15—Hot isostatic pressing
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C14/00—Alloys based on titanium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/16—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of other metals or alloys based thereon
- C22F1/18—High-melting or refractory metals or alloys based thereon
- C22F1/183—High-melting or refractory metals or alloys based thereon of titanium or alloys based thereon
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- Mechanical Engineering (AREA)
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- Manufacturing & Machinery (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Powder Metallurgy (AREA)
Abstract
本发明涉及一种Ti‑Fe合金基复合材料及其制备方法，属于复合材料制备技术领域。本发明以Ti粉、Fe粉和B4C粉为原料，将一定量的Ti粉、Fe粉和B4C粉混合后装入不锈钢包套，经过振实、除气、封口、热等静压烧结以及机加工去除包套等工序，得到TiC+TiB颗粒增强的Ti‑Fe合金基复合材料。本发明通过控制工艺参数和材料成分，保证Ti‑Fe合金基复合材料增强相分布均匀、致密度高、力学性能好。采用粉末冶金的制备方法，工艺路线简单，制备周期短，成本低，可实现大规模的工业应用。实施例结果证明，本发明提供的Ti‑Fe合金基复合材料在室温下抗压强度在1700～1900MPa，压缩弹性模量在8～9GPa。
The invention relates to a Ti-Fe alloy-based composite material and a preparation method thereof, belonging to the technical field of composite material preparation. The present invention uses Ti powder, Fe powder and B 4 C powder as raw materials, mixes a certain amount of Ti powder, Fe powder and B 4 C powder into a stainless steel package, and undergoes vibrating, degassing, sealing, thermal isostatic Press sintering and machining to remove the jacket, etc., to obtain a Ti-Fe alloy matrix composite material reinforced by TiC+TiB particles. By controlling process parameters and material components, the invention ensures uniform distribution of the reinforcing phase of the Ti-Fe alloy-based composite material, high density and good mechanical properties. The powder metallurgy preparation method has the advantages of simple process route, short preparation period and low cost, and can realize large-scale industrial application. The results of the examples prove that the compressive strength of the Ti-Fe alloy-based composite material provided by the present invention is 1700-1900 MPa at room temperature, and the compressive elastic modulus is 8-9 GPa.
Description
Technical Field
The invention relates to the technical field of composite material preparation, and particularly relates to a Ti-Fe alloy based composite material and a preparation method thereof.
Background
With the rapid development of the technology in the field of biomedical materials, the traditional pure Ti and Ti-6Al-4V alloys are more and more difficult to meet the requirements of human body implant materials, and the development of novel titanium alloys which are non-toxic, good in biocompatibility and low in elastic modulus is becoming the key research direction in the field.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide a Ti-Fe alloy based composite material which has high compactness, better reinforcing effect and better wear resistance.
The invention also aims to provide a preparation method of the Ti-Fe alloy based composite material, which has the advantages of simple process route, short preparation period and low cost and can realize large-scale industrial application.
The technical problem to be solved by the invention is realized by adopting the following technical scheme.
The invention provides a preparation method of a Ti-Fe alloy based composite material, which comprises the following steps:
mixing Ti powder, Fe powder and B4And degassing the mixed powder of the C powder in vacuum, and sintering by adopting a hot isostatic pressing method.
1-15% of Fe powder and B40.18-1.8% of C powder, and the balance of Ti powder and inevitable impurities.
The invention provides a Ti-Fe alloy based composite material, which is prepared by the preparation method of the Ti-Fe alloy based composite material.
The beneficial effects of the invention include:
the invention uses iron powder, titanium powder and B4The powder C is used as a raw material, a Ti-Fe alloy based composite material is prepared by a powder metallurgy method, powder densification and in-situ authigenic reaction triggering are combined through hot isostatic pressing sintering, and the TiC + TiB particle reinforced Ti-Fe alloy based composite material is prepared and has high density and high compression strength. Experimental results prove that the density of the Ti-Fe alloy-based composite material obtained by the preparation method provided by the invention reaches over 99.5%, the compression strength reaches 1860MPa, and the compression elastic modulus is 8.6 GPa. The preparation method has the advantages of simple process route, short preparation period and low cost, and can realize large-scale industrial application.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings needed to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
FIG. 1 is a sectional scanning electron microscope of a Ti-Fe alloy-based composite material provided in example 1 of the present invention;
FIG. 2 is a scanning electron microscope view of a fracture of the Ti-Fe alloy-based composite material provided in example 1 of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention clearer, the technical solutions in the embodiments of the present invention will be clearly and completely described below. The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially.
The titanium-based composite material has higher specific strength, specific stiffness, wear resistance and high temperature resistance than the traditional titanium alloy by introducing the second-phase reinforcement into the titanium alloy matrix, and has great application prospect in various fields such as aerospace, marine ships, automobile manufacturing, energy chemical industry, biomedical treatment and the like. From the view of the preparation method of the titanium-based composite material, at present, a fusion casting method, a mechanical alloying method, a self-propagating high-temperature synthesis method, a powder metallurgy method and the like are mainly adopted.
The powder metallurgy method for preparing the titanium-based composite material in the temperature range lower than the melting point of the titanium alloy can not only avoid the problem of high reaction of liquid titanium in the casting method, but also effectively improve the defects of material organization, component segregation, large crystal grains and the like caused by the casting method, can realize the adjustment of the particle size and the volume fraction of the particle reinforced phase in a larger range, and is a preparation method of the titanium-based composite material with great development prospect.
From the aspect of the enhanced phase adding mode, the external addition method and the in-situ self-generation method are mainly used. The particles of the external addition method are relatively coarse, and the pollution problem exists between the particles and the interface of the matrix. The in-situ self-generated particle reinforced phase avoids the chemical problem between reinforced particles and an interface, has no pollution with the surface of a matrix and high bonding strength, and is one of the important directions of the research of the titanium-based composite material at present.
Although the conventional powder metallurgy method can be used for preparing Ti-Fe alloy based composite materials, the obtained compactness is still not high. The invention provides a preparation method of a Ti-Fe alloy-based composite material, which can be used for preparing the composite material with high density, better reinforcing effect and wear resistance.
The Ti-Fe alloy-based composite material and the method for preparing the same according to the embodiments of the present invention will be described in detail below.
The invention provides a Ti-Fe alloy based composite material, which comprises the following components:
mixing Ti powder, Fe powder and B4Vacuum degassing is carried out on the mixed powder of the C powder, and then sintering is carried out by adopting a hot isostatic pressing method; 1-15% of Fe powder and B40.18-1.8% of C powder, and the balance of Ti powder and inevitable impurities.
The addition of the iron powder improves the strength and hardness of the composite material. However, when the content of the iron powder is too high, a liquid phase is generated in the sintering process, and the sintering quality is affected. When the content of the iron powder is 1-15%, no liquid phase occurs, and the obtained composite material has good strength and hardness. Alternatively, the iron powder content may be 2%, 3%, 4%, 11%, 13%. Further, the content of the iron powder may be 5 to 10%, wherein the content of the iron powder may be 6%, 7%, 8%, 9%.
B4The C powder is used as an in-situ reactant and generates TiC + TiB particles with the titanium powder to enhance the strength and hardness of the Ti-Fe alloy matrix composite material. In order to ensure even distribution and high density of the reinforcing phase, B4The content of the C powder is 0.18-1.8%, wherein the content can be 0.2%, 0.3%, 1.3%, 1.5% and 1.7%. Further, the content of the iron powder may be 0.5 to 1.0%. Wherein the content can be 0.6%, 0.8%, 0.9%. Within this content range, B4The addition of the powder C can not cause the composite material to become brittle, and the mechanical property of the composite material is enhanced.
In some embodiments of the invention, Ti powder andthe grain diameter of the Fe powder is not larger than 325 meshes. The Ti powder and the Fe powder in the particle size range can be fully mixed, the problem of poor density caused by high sintering activity is avoided, the requirement on sintering temperature is high if the particle size is large, and the cost and the sintering condition are improved. In order to ensure the quality of the composite material, Ti powder, Fe powder and B4The purity of the C powder is more than 99 percent.
Specifically, Ti powder, Fe powder and B powder are weighed according to the proportion4And C, putting the powder C into a three-dimensional mixer, and mixing for 3-5 hours to obtain mixed powder.
Filling the mixed powder into a prepared stainless steel ladle sleeve, compacting, and keeping the vacuum degree below 10-1Pa, and the temperature is 600-700 ℃ for vacuum degassing treatment. And sealing the sheath.
And (4) placing the sealed sheath into hot isostatic pressing, and sintering by adopting the hot isostatic pressing method. Heating to 960-1050 ℃, carrying out heat preservation and pressure maintaining sintering for 1-3 hours under the pressure condition of 120-150 MPa, and then cooling along with the furnace. It should be noted that the heating rate is not higher than 10 ℃/min, so as to ensure the sufficient reaction of the mixed powder, and to make the reinforcing phase distributed uniformly, the density high, and the mechanical property good. Optionally, the sintering temperature is 970 ℃, 980 ℃, 990 ℃ and 1000 ℃. The sintering pressure is 130-140 MPa.
And removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
The invention is realized by adopting B4The powder C is used as a raw material, the proportion of the raw materials is controlled, the process parameters are controlled, and the powder densification and the in-situ spontaneous reaction triggering are combined through hot isostatic pressing sintering to prepare the TiC + TiB particle reinforced Ti-Fe alloy based composite material which has higher density and higher compression strength.
The features and properties of the present invention are described in further detail below with reference to examples.
Example 1
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-5wt% Fe-0.9wt% B4C mass ratio, removing hydrogenationTitanium hydride powder, carbonyl iron powder and B4C, putting the powder C into a three-dimensional mixer for mixing for 3-5 hours to obtain mixed powder;
the mixed powder is filled into a prefabricated stainless steel ladle sleeve, is manually compacted, is degassed at the temperature of 600-700 ℃ in vacuum, and is vacuumized to be lower than 10 DEG C-1Pa, and then welding the sheath opening to seal;
placing the sealed sheath into hot isostatic pressing, heating at the speed of 10 ℃/min, keeping the temperature and the pressure for 1-3 hours at the temperature of 960-1050 ℃ and the air pressure of 120-150 MPa, and then cooling along with a furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
The microstructure test of the Ti-Fe alloy based composite material shows that the compactness is 99.5%, the section microstructure of the composite material is shown in figure 1, the fracture section is shown in figure 2, the figure shows that the composite material has compact structure and fine grain size, the matrix is (α + β) Ti, the reinforced phase is uniformly distributed, and no obvious holes exist.
The mechanical property test is carried out on the Ti-Fe alloy based composite material, the room temperature compression strength is 1860MPa, and the compression elastic modulus is 8.6 GPa.
Example 2
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-1 wt% Fe-0.18 wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder into a three-dimensional mixer for mixing for 3 hours to obtain mixed powder;
loading the mixed powder into a stainless steel jacket prepared in advance, manually compacting, degassing at 600 deg.C, and vacuumizing to below 10 ℃-1Pa, and then welding the sheath opening to seal;
putting the sealed sheath into hot isostatic pressing, heating at the speed of 8 ℃/min, keeping the temperature and the pressure for 1 hour at the temperature of 960 ℃ and the air pressure of 120MPa, and then cooling along with the furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
And microstructure test is carried out on the Ti-Fe alloy-based composite material, and the density is 98%. The mechanical property test is carried out on the Ti-Fe alloy-based composite material, the room temperature compressive strength is 1730MPa, and the compressive elastic modulus is 8.1 GPa.
Example 3
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-15 wt% Fe-1.8 wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder into a three-dimensional mixer for mixing for 5 hours to obtain mixed powder;
loading the mixed powder into a stainless steel jacket prepared in advance, manually compacting, degassing at 700 deg.C, and vacuumizing to below 10 ℃-1Pa, and then welding the sheath opening to seal;
putting the sealed sheath into hot isostatic pressing, heating at the speed of 9 ℃/min, keeping the temperature and pressure for 3 hours at 1050 ℃ and 150MPa, and then cooling along with the furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
And microstructure test is carried out on the Ti-Fe alloy-based composite material, and the compactness is 99%. The Ti-Fe alloy based composite material is subjected to mechanical property test, the room temperature compression strength is 1902MPa, and the compression elastic modulus is 8.9 GPa.
Example 4
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-5wt% Fe-0.5 wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder into a three-dimensional mixer for mixing for 3 hours to obtain mixed powder;
loading the mixed powder into a stainless steel jacket prepared in advance, manually compacting, degassing at 650 deg.C, and vacuumizing to less than 10 ℃-1Pa, and then welding the sheath opening to seal;
putting the sealed sheath into hot isostatic pressing, heating at the speed of 10 ℃/min, keeping the temperature and the pressure for 2 hours at the temperature of 1000 ℃ and the air pressure of 130MPa, and then cooling along with the furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
And microstructure test is carried out on the Ti-Fe alloy-based composite material, and the density is 99.2%. The mechanical property test is carried out on the Ti-Fe alloy based composite material, the room temperature compressive strength is 1800MPa, and the compressive elastic modulus is 8.2 GPa.
Example 5
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-10 wt% Fe-1.0 wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder into a three-dimensional mixer for mixing for 4 hours to obtain mixed powder;
the mixed powder is filled into a prefabricated stainless steel ladle sleeve, is manually compacted, is degassed at the temperature of 600-700 ℃ in vacuum, and is vacuumized to be lower than 10 DEG C-1Pa, and then welding the sheath opening to seal;
putting the sealed sheath into hot isostatic pressing, heating at the speed of 10 ℃/min, keeping the temperature and the pressure at 980 ℃ and 140MPa for 1-3 hours, and then cooling along with a furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
And microstructure test is carried out on the Ti-Fe alloy-based composite material, and the density is 99.2%. The mechanical property test is carried out on the Ti-Fe alloy-based composite material, the room temperature compressive strength is 1890MPa, and the compressive elastic modulus is 8.7 GPa.
Example 6
The embodiment provides a Ti-Fe alloy based composite material, which is mainly prepared by the following steps:
according to Ti-8 wt% Fe-0.8 wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder into a three-dimensional mixer for mixing for 4 hours to obtain mixed powder;
loading the mixed powder into a stainless steel jacket prepared in advance, manually compacting, degassing at 700 deg.C, and vacuumizing to below 10 ℃-1Pa, and then welding the sheath opening to seal;
putting the sealed sheath into hot isostatic pressing, heating at the speed of 10 ℃/min, keeping the temperature and pressure for 2 hours at 1050 ℃ and 150MPa, and then cooling along with the furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy based composite material.
And microstructure test is carried out on the Ti-Fe alloy-based composite material, and the density is 99.4%. The mechanical property test is carried out on the Ti-Fe alloy-based composite material, the room temperature compression strength is 1840MPa, and the compression elastic modulus is 8.4 GPa.
The embodiments described above are some, but not all embodiments of the invention. The detailed description of the embodiments of the present invention is not intended to limit the scope of the invention as claimed, but is merely representative of selected embodiments of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Claims (2)
1. A preparation method of a Ti-Fe alloy based composite material is characterized by comprising the following steps:
according to Ti-5wt% Fe-0.9wt% B4C, mixing hydrogenated dehydrogenated titanium powder, carbonyl iron powder and B4C, putting the powder C into a three-dimensional mixer for mixing for 3-5 hours to obtain mixed powder;
the mixed powder is filled into a prefabricated stainless steel ladle sleeve, is manually compacted, is degassed at the temperature of 600-700 ℃ in vacuum, and is vacuumized to be lower than 10 DEG C-1Pa, and then welding the sheath opening to seal;
placing the sealed sheath into hot isostatic pressing, heating at the speed of 10 ℃/min, keeping the temperature and the pressure for 1-3 hours at the temperature of 960-1050 ℃ and the air pressure of 120-150 MPa, and then cooling along with a furnace;
and removing the stainless steel sheath on the surface by machining to obtain the Ti-Fe alloy-based composite material, wherein the density of the Ti-Fe alloy-based composite material reaches over 99.5 percent, the compressive strength reaches 1860MPa, and the compressive elastic modulus is 8.6 GPa.
2. The Ti-Fe alloy-based composite material is characterized by being prepared by the preparation method of the Ti-Fe alloy-based composite material according to claim 1, wherein the compactness of the Ti-Fe alloy-based composite material reaches more than 99.5 percent, the compressive strength reaches 1860MPa, and the compressive elastic modulus is 8.6 GPa.
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Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101921930A (en) * | 2010-09-16 | 2010-12-22 | 上海交通大学 | Multi-component microalloyed titanium alloy and preparation method thereof |
| CN103305781A (en) * | 2013-07-09 | 2013-09-18 | 上海交通大学 | Multi-element microalloyed titanium alloy processing method |
| CN103572186A (en) * | 2013-10-14 | 2014-02-12 | 上海交通大学 | Method for preparing ultra-fine grain titanium-based composite material by adopting equant bending channel deformation |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN1122114C (en) * | 2001-03-23 | 2003-09-24 | 中国科学院金属研究所 | High-strnegth Ti-base composition reinforced by in-situ combination of crystal whiskers with particles |
| CN105088014B (en) * | 2015-09-15 | 2017-04-05 | 北京工业大学 | A kind of low-cost high-strength Ti Fe alloy blanks and its preparation technology |
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Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101921930A (en) * | 2010-09-16 | 2010-12-22 | 上海交通大学 | Multi-component microalloyed titanium alloy and preparation method thereof |
| CN103305781A (en) * | 2013-07-09 | 2013-09-18 | 上海交通大学 | Multi-element microalloyed titanium alloy processing method |
| CN103572186A (en) * | 2013-10-14 | 2014-02-12 | 上海交通大学 | Method for preparing ultra-fine grain titanium-based composite material by adopting equant bending channel deformation |
Non-Patent Citations (2)
| Title |
|---|
| Fabrication of TiC and TiB2 locally reinforced steel matrix composites using a Fe–Ti–B4C–C system by an SHS-casting route;Zhiqiang Zhang;《Journal of Materials Science》;20071001;第8350-8355页 * |
| Fe-Ti-B4C体系SHS反应制备TiC-TiB2局部增强低Cr钢基复合材料;张志强;《中国优秀硕士学位论文全文数据库 工程科技Ⅰ辑》;20070515(第5期);第B020-7页 * |
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