CN111004955A - TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material - Google Patents
TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material Download PDFInfo
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- 230000007797 corrosion Effects 0.000 title claims abstract description 75
- 238000005260 corrosion Methods 0.000 title claims abstract description 75
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 67
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 67
- 239000000463 material Substances 0.000 title claims abstract description 50
- 239000007788 liquid Substances 0.000 title claims abstract description 49
- 229910018487 Ni—Cr Inorganic materials 0.000 title claims abstract description 24
- 239000004411 aluminium Substances 0.000 title claims abstract description 10
- 239000000843 powder Substances 0.000 claims abstract description 85
- 229910033181 TiB2 Inorganic materials 0.000 claims abstract description 45
- 238000000498 ball milling Methods 0.000 claims abstract description 18
- 238000001035 drying Methods 0.000 claims abstract description 12
- 238000002490 spark plasma sintering Methods 0.000 claims abstract description 12
- 239000002994 raw material Substances 0.000 claims abstract description 6
- 238000005245 sintering Methods 0.000 claims description 31
- 238000010438 heat treatment Methods 0.000 claims description 9
- 239000002245 particle Substances 0.000 claims description 7
- 239000011812 mixed powder Substances 0.000 claims description 6
- 238000004321 preservation Methods 0.000 claims description 2
- 229910052751 metal Inorganic materials 0.000 description 18
- 239000002184 metal Substances 0.000 description 17
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 14
- 238000000034 method Methods 0.000 description 12
- 239000011159 matrix material Substances 0.000 description 11
- 238000002360 preparation method Methods 0.000 description 11
- 238000009792 diffusion process Methods 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 8
- 238000002156 mixing Methods 0.000 description 7
- 238000001878 scanning electron micrograph Methods 0.000 description 7
- 239000011195 cermet Substances 0.000 description 6
- 229910052759 nickel Inorganic materials 0.000 description 6
- 230000008569 process Effects 0.000 description 6
- 229910052742 iron Inorganic materials 0.000 description 5
- 239000000919 ceramic Substances 0.000 description 4
- 238000005520 cutting process Methods 0.000 description 4
- 238000002474 experimental method Methods 0.000 description 4
- 229910001018 Cast iron Inorganic materials 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000000956 alloy Substances 0.000 description 3
- 230000003628 erosive effect Effects 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 238000007747 plating Methods 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- LFQSCWFLJHTTHZ-UHFFFAOYSA-N Ethanol Chemical compound CCO LFQSCWFLJHTTHZ-UHFFFAOYSA-N 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 150000002739 metals Chemical class 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 238000001272 pressureless sintering Methods 0.000 description 2
- 239000010935 stainless steel Substances 0.000 description 2
- 229910001220 stainless steel Inorganic materials 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000001291 vacuum drying Methods 0.000 description 2
- 244000137852 Petrea volubilis Species 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- 230000002411 adverse Effects 0.000 description 1
- 238000005269 aluminizing Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 239000013590 bulk material Substances 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 229910010293 ceramic material Inorganic materials 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000009770 conventional sintering Methods 0.000 description 1
- 238000001816 cooling 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
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/14—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on borides
-
- 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
- C22C1/051—Making hard metals based on borides, carbides, nitrides, oxides or silicides; Preparation of the powder mixture used as the starting material therefor
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F3/00—Manufacture of workpieces or articles from metallic powder characterised by the manner of compacting or sintering; Apparatus specially adapted therefor ; Presses and furnaces
- B22F3/10—Sintering only
- B22F3/105—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding
- B22F2003/1051—Sintering only by using electric current other than for infrared radiant energy, laser radiation or plasma ; by ultrasonic bonding by electric discharge
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- Metallurgy (AREA)
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Abstract
The invention discloses a TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, with TiB2Powder, Fe powder, Co powder, Ni powder and Cr powder are taken as raw materials, and the material is prepared by ball milling, drying and spark plasma sintering; the TiB2The Fe-Co-Ni-Cr aluminum liquid corrosion resistant material is easy to prepare and has excellent aluminum corrosion resistance.
Description
Technical Field
The invention belongs to the field of aluminum liquid corrosion resistant materials, and particularly relates to a TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material.
Background
At present, aluminum and its alloy are widely used in the fields of traffic, energy, electronics, etc. But the aluminum liquid is one of the most corrosive metal liquids, so that equipment directly contacting the aluminum liquid is greatly corroded in a smelting, casting and hot-dip aluminizing production line, and the service life of the equipment is greatly shortened. And the dissolution of the materials in the aluminum liquid may pollute the aluminum liquid, so that the product quality is low, and the production efficiency is influenced. In a hot-dip aluminum plating production line, equipment such as an aluminum liquid loading tank, an immersion roller and the like needs to be soaked in aluminum liquid for a long time, so that the service life of the hot-dip aluminum plating production equipment is shortened, the quality of a plating layer is reduced, the energy consumption is increased, the production efficiency is reduced and other adverse effects are caused. Therefore, the aluminum liquid corrosion resistance of the material is improved, and a series of corrosion problems such as aluminum liquid pollution, corrosion perforation of an aluminum liquid containing container, aluminum sticking of an aluminum forming die and the like can be effectively solved.
Therefore, a new material resistant to molten aluminum corrosion needs to be designed.
Disclosure of Invention
The technical problem to be solved by the invention is to provide a TiB2-Fe-Co-Ni-Cr Al-Si-Al-Ti-Al2The Fe-Co-Ni-Cr aluminum liquid corrosion resistant material has excellent aluminum liquid corrosion resistance.
The technical solution of the invention is as follows:
TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, with TiB2Powder, Fe powder, Co powder, Ni powder and Cr powder are taken as raw materials, and the material is prepared by ball milling, drying and sintering;
the raw materials comprise the following components in percentage by mass:
TiB270-88% of powder, 2.97-7.43% of Fe powder, 3.14-7.84% of Co powder, 3.12-7.81% of Ni powder and 2.77-6.92% of Cr powder.
The TiB2Purity of the powder>99.5% of particle size<35 microns.
The purity of the Fe powder, the Co powder, the Ni powder and the Cr powder is more than 99.9 percent, and the granularity is less than 15 microns.
TiB2The powder content is 80-88%.
The Fe powder accounts for 2.97-4.95%.
The content of Co powder is 3.14-5.23%.
3.12 to 5.21 percent of Ni powder.
The Cr powder accounts for 2.77-4.61%.
Spark plasma sintering refers to: and (3) placing the dried mixed powder into a mold, heating to the temperature T at the temperature T of 1300-1400 ℃ at the heating rate of 300 ℃/min of 200 ℃/min-300 ℃/min, and preserving the heat for 5-10 minutes in the temperature T environment at the pressure of 50-60 MPa.
The heating rate is 200 ℃/min, 250 ℃/min or 300 ℃/min;
t is 1300 ℃, 1350 ℃ or 1400 ℃, and the heat preservation time is 5, 7, 8, 9 or 10 minutes.
The sintering adopts spark plasma sintering.
The preparation method comprises the following steps:
TiB2The preparation method of the Fe-Co-Ni-Cr molten aluminum corrosion resistant material comprises the following steps:
step 1: mixing and ball milling:
weighing TiB according to preset mass percentage2Putting the powder, Fe powder, Co powder, Ni powder and Cr powder into a ball mill for ball milling;
TiB2the powder comprises the following components in percentage by mass: TiB270-88% of powder, 2.97-7.43% of Fe powder, 3.14-7.84% of Co powder, 3.12-7.81% of Ni powder and 2.77-6.92% of Cr powder.
Step 2: and (3) drying:
putting the ball-milled powder into a vacuum drying box for drying;
and step 3: sintering:
and putting the dried mixed powder into a mould for spark plasma sintering.
The ball mill in the step 1
The method is characterized in that the wet ball milling is carried out, absolute ethyl alcohol is used as a ball milling medium, and the ball: the mixing powder ratio is 3:1, the grinding balls and the mixing powder are added according to the mass ratio of 3:1-5:1 (preferably 3:1), the rotating speed is 150-. The ball milling tank and the milling balls are made of hard alloy.
In the drying step in the step 2, the drying temperature is 70-90 ℃, the vacuum degree is 0.09MPa to-0.1 MPa, the preferred vacuum degree is-0.1 MPa, and the drying time is 8-12 hours, and the preferred time is 12 hours.
The sintering can be completed by pressureless sintering, hot-pressing sintering, spark plasma sintering and the like; however, the use of Spark Plasma Sintering (SPS) has the following advantages over conventional sintering processes (pressureless sintering, hot pressed sintering, etc.): the method has the characteristics of high heating rate, low sintering temperature, short sintering time and the like, can prepare high-density materials at a lower temperature, is commonly used for preparing ceramic materials difficult to sinter, generates discharge plasma when the electrode is introduced with direct-current pulse current in the sintering process, purifies the surfaces of particles, and enables each particle to uniformly generate Joule heat per se and activate the surfaces of the particles. Therefore, the sintering can be completed quickly and efficiently, the energy is saved, the production cost is reduced, and the production efficiency is improved.
The spark plasma sintering can be carried out by FAS-10015Y spark plasma sintering equipment or other equipment manufactured by Shanghai Kangshi electric furnace equipment Co.
Description of the technical idea of the invention TiB2Has a plurality of excellent performances such as high hardness, high wear resistance, good high-temperature oxidation resistance and the like. But TiB2Poor high-temperature toughness, low diffusion coefficient and poor sintering property, so that the pure TiB2Sintering preparation of the material is difficult. Therefore, the characteristics of excellent toughness and low melting point of the metal binding phase can be utilized to improve TiB2Poor toughness and difficult sintering. But TiB2The wettability with most metals is poor, so it is necessary to select one with TiB2The metal with good wettability is used as a binding phase. The related literature is consulted to find that only Fe, Co, Ni and TiB2Has better wettability, so the elements Fe, Co and Ni are selectively added to improve the TiB2The addition of Cr element has a good strengthening effect, and the addition of metal element can improve TiB2The brittleness and the toughness of the steel are improved.
Has the advantages that:
the invention discloses a TiB2Fe-Co-Ni-Cr-Ti aluminum liquid corrosion resistant metal ceramic monolithic material is prepared byTiB2The ceramic powder is added with metal simple substance as a binding phase, thereby obviously reducing TiB2The sintering temperature of the alloy improves TiB2Sintering property of (2). And compared with the traditional sintering process, the spark plasma sintering process has great advantages, can obviously reduce the sintering temperature and the sintering time, and has the characteristics of low temperature, rapidness and high efficiency. Meanwhile, the preparation process is simple, the price is low, the excellent corrosion resistance is shown in the aluminum liquid, and the preparation method has important application value in industry.
TiB2As the only stable compound of the transition group metal elements Ti and B, having a close-packed hexagonal C32 type crystal structure, TiB2Meanwhile, the wear-resistant steel has strong Ti-B ionic bonds and B-B covalent bonds, so that the wear-resistant steel has high hardness, high wear resistance and good high-temperature oxidation resistance. But TiB2Poor high-temperature toughness, low diffusion coefficient and poor sintering property, so that the pure TiB2Sintering preparation of the material is difficult. Therefore, the characteristics of excellent toughness and low melting point of the metal binding phase can be utilized to improve TiB2Poor toughness and difficult sintering. But TiB2The wettability with most metals is poor, so that it is necessary to select a metal having good wettability with the metal as a binder phase. Therefore, a new metal system is designed as a binding phase, and a new sintering process is designed to improve TiB2The material has the defect of difficult sintering, has excellent aluminum liquid corrosion resistance, low price of raw materials, simple preparation process and considerable industrial application prospect.
At present, the average corrosion rate of the cast iron material commonly used in the production industry in molten aluminum at 700 ℃ is 8.5 multiplied by 10-1The average corrosion rate of mm/h, 316L stainless steel in aluminum liquid at 700 ℃ is 1.1 multiplied by 10-1mm/h. In the first embodiment of the invention, the average corrosion rate of the material is 5.13 multiplied by 10-3mm/h, compared with the common cast iron and 316L stainless steel in the current industrial production, the aluminum liquid corrosion resistance is greatly improved, and the test proves that TiB in the material2The higher the content is, the better the corrosion resistance of the material is, and the material has good industrial application prospect.
Drawings
FIG. 1 shows TiB in the first embodiment of the present invention2SEM image of the mixed powder of-Fe-Co-Ni-Cr after ball milling.
FIG. 2 shows TiB prepared in the first embodiment of the present invention2SEM image of-Fe-Co-Ni-Cr cermet bulk Material
FIG. 3 shows TiB prepared in the second embodiment of the present invention2SEM image of Fe-Co-Ni-Cr cermet monolith.
FIG. 4 shows TiB prepared in the third embodiment of the present invention2SEM image of Fe-Co-Ni-Cr cermet monolith.
FIG. 5 is a graph of etch depth versus time for three different materials in an embodiment of the present invention.
FIG. 6 is an SEM image of a corrosion interface of the material after 2, 4, 6, 8 and 10 days of corrosion in molten aluminum at 700 ℃ in the first embodiment of the invention.
Detailed Description
In order to facilitate an understanding of the invention, the invention will be described more fully and in detail below with reference to the accompanying drawings and preferred embodiments, but the scope of the invention is not limited to the following specific embodiments.
Unless otherwise defined, all terms of art used hereinafter have the same meaning as commonly understood by one of ordinary skill in the art. The terminology used herein is for the purpose of describing particular embodiments only and is not intended to limit the scope of the present invention.
Example 1:
the first embodiment is as follows: TiB2The preparation method of the Fe-Co-Ni-Cr aluminum liquid corrosion resistant metal ceramic integral material comprises the following steps:
(1) sample preparation: mixing TiB2Fe, Co, Ni and Cr powder are weighed according to the following mass percent: TiB270% of powder, 7.43% of Fe powder, 7.84% of Co powder, 7.81% of Ni powder and 6.92% of Cr powder. The TiB2The purity of the powder was 99.5%, particle size<35 microns; the purity of the Fe powder, the Co powder, the Ni powder and the Cr powder>99.9% by weight, particle size<15 microns.
(2) Ball milling: putting the weighed mixture into a ball milling tank, and mixing according to the ballThe material mass ratio is 3:1, and the required balls are weighed and placed into a ball milling tank. And (3) adopting a wet ball milling process, and pouring a proper amount of absolute ethyl alcohol into the ball milling tank to cover the powder. The rotating speed of the ball mill is 200r/min, and the ball milling time is 1 hour. FIG. 1 is an SEM image of the mixed powder after ball milling. It can be seen from the figure that after the ball milling of the mixed powder, the metal powder is uniformly dispersed in the TiB2In the powder.
(3) And (3) drying: and (3) putting the mixed slurry subjected to ball milling into a vacuum drying oven for drying, wherein the temperature of the drying oven is 70-90 ℃, the vacuum degree is-0.1 MPa, and the drying time is 12 hours. The dried powder was taken out for further use.
(4) And (3) sintering: the sintering equipment used in this example was spark plasma sintering, and the dried powder was placed in a cylindrical graphite mold and then sintered in the sintering equipment, and the sintering process was set as follows: heating from room temperature to 1400 deg.C at 300 deg.C/min, maintaining at 1400 deg.C for 5 min, and pressurizing at 50-60MPa during sintering. And cooling along with the furnace after sintering is finished, and then demoulding to obtain a sample. FIG. 2 is a microscopic topography of a sample under a Scanning Electron Microscope (SEM). From the SEM image, it can be seen that the dark gray is TiB2Hard phase, light gray is metal binding phase distributed in TiB2Around the hard phase, TiB is filled2The surrounding void.
And cutting the prepared sample into cuboid samples with the size of 4 multiplied by 5 multiplied by 10mm by using an electric spark numerical control wire cutting machine, and cutting 5 samples, wherein the cutting position is preferably the central position of the sample. And (4) polishing the surface of the sample by using sand paper, and removing an oxide film on the surface of the sample. And then measuring the thickness of the sample before corrosion by using a micrometer, then putting the sample into a graphite crucible filled with aluminum liquid at 700 ℃ for a corrosion experiment, heating and preserving heat by using a well-type resistance furnace, respectively corroding for 2 days, 4 days, 6 days, 8 days and 10 days, then taking out, analyzing the texture of a corrosion interface by using a Scanning Electron Microscope (SEM), and measuring the phased chemical components by using an energy spectrometer (EDS).
The corrosion depth and the corrosion rate of the sample at different time are calculated, the corrosion rate is measured by using a depth method in the experiment, and the calculation formula is as follows: v ═ a-b)/2 t.
And a is the thickness of the sample before corrosion, b is the thickness of the sample after corrosion, t is corrosion time, the thickness a before corrosion is accurately measured by a micrometer before a corrosion experiment, then the structural observation is carried out on the cross section of the sample after corrosion under a scanning electron microscope, and the residual thickness b of the sample after corrosion is measured by Smile View software.
Example two: compared with the first embodiment, the method of the second embodiment is the same except that the step (1) is different; step (1) of example two, sample preparation: mixing TiB2Fe, Co, Ni and Cr powder are weighed according to the following mass percent: TiB288% of powder, 2.97% of Fe powder, 3.14% of Co powder, 3.12% of Ni powder and 2.77% of Cr powder. The other steps are the same as in the first embodiment. FIG. 3 is a SEM microstructure of sintered sample of this example. The erosion depth of this material as a function of time is shown in FIG. 5.
Example three: compared with the method in the first embodiment, the method in the third embodiment is the same except that the step (1) is different; step (1) of example three, sample preparation: mixing TiB2Fe, Co, Ni and Cr powder are weighed according to the following mass percent: TiB280% of powder, 4.95% of Fe powder, 5.23% of Co powder, 5.21% of Ni powder and 4.61% of Cr powder. The other steps are the same as in the first embodiment. FIG. 4 is a SEM microstructure of sintered sample of this example. The erosion depth of this material as a function of time is shown in FIG. 5.
FIG. 5 is a graph showing the erosion depth of three materials of the first, second and third embodiments as a function of time. It can be seen from the figure that the etch depth of this material increases with the time of etching, but the etch rate decreases with time. The average corrosion rate of the cermet material in the first example was calculated as: 5.13X 10-3mm/h; the average corrosion rate of the cermet material in example two was: 2.901X 10-3mm/h; the average corrosion rate of the cermet material in example three was: 7.883X 10-3mm/h. Compared with the corrosion rate of cast iron in molten aluminum of 0.85mm/h, the corrosion rate of the molten aluminum resistance of the integral material is greatly improved.
FIG. 6 shows aluminum at 700 ℃ for one embodiment of the materialSEM images of the corrosion interface after 2, 4, 6, 8, and 10 days of in-liquid corrosion (corresponding to FIGS. 6(a) to (e), respectively). The substrate, the corrosion layer and the aluminum layer are sequentially arranged from left to right. The picture after 2 days of corrosion shows that the aluminum liquid begins to corrode the matrix, and the preferential corrosion is the metal binding phase, TiB2The ceramic phase is present in the molten aluminum without being corroded. The depth of the etch layer increases as the etch time increases. A diffusion layer which is denser than the matrix is found between the corrosion layer and the matrix, EDS analysis shows that the aluminum content of the diffusion layer is obviously less than that of the corrosion layer, and the aluminum content is lower at the position closer to the matrix, which indicates that the diffusion layer effectively slows down the corrosion of aluminum liquid to the matrix. Through comparing the electron microscope photos after 2, 4, 6, 8 and 10 days of corrosion, the wettability of the external aluminum liquid and the material is poor in the early stage of corrosion, a gap exists between the aluminum liquid and the corrosion layer, the gap between the aluminum liquid and the corrosion layer is reduced along with the prolonging of corrosion time, and the picture after 10 days of corrosion shows that the aluminum liquid and the corrosion layer are tightly combined. And in experiments, the aluminum liquid corrodes the material, but the corrosion layer is not separated from the matrix and is dissociated in the aluminum liquid, and the material still maintains the original shape.
TiB2Has high melting point, high hardness, high wear resistance and good high-temperature oxidation resistance, has poor wettability with aluminum liquid and does not react with the aluminum liquid. It can be found by the examples that the aluminium liquid will preferentially corrode the metal binding phase, TiB2The phases are not corroded by the molten aluminum and still exist in the matrix. As the corrosion time increases, a diffusion layer denser than the matrix is found between the corrosion layer and the matrix, and EDS analysis shows that the aluminum content of the diffusion layer is obviously less than that of the corrosion layer, and the aluminum content is lower at the position closer to the matrix, which indicates that the diffusion layer effectively slows down the corrosion of aluminum liquid to the matrix, and the corrosion rate is also determined as follows: as the etch time increases, the etch rate decreases.
The embodiments are only for the purpose of facilitating understanding of the technical solutions of the present invention, and do not constitute a limitation to the scope of the present invention, and any simple modification, equivalent change and modification made to the above solutions without departing from the contents of the technical solutions of the present invention or the technical spirit of the present invention still fall within the scope of the present invention.
Claims (10)
1. TiB2-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, characterized in that TiB is used2Powder, Fe powder, Co powder, Ni powder and Cr powder are taken as raw materials, and the material is prepared by ball milling, drying and sintering;
the raw materials comprise the following components in percentage by mass:
TiB270-88% of powder, 2.97-7.43% of Fe powder, 3.14-7.84% of Co powder, 3.12-7.81% of Ni powder and 2.77-6.92% of Cr powder.
2. The TiB of claim 12-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, characterized in that said TiB2Purity of the powder>99.5% of particle size<35 microns;
the purity of the Fe powder, the Co powder, the Ni powder and the Cr powder is more than 99.9 percent, and the granularity is less than 15 microns.
3. The TiB of claim 12-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that TiB2The powder content is 80-88%.
4. The TiB of claim 12-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that the Fe powder is 2.97-4.95%.
5. The TiB of claim 12-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that Co powder is 3.14-5.23%.
6. The TiB of claim 12-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that Ni powder is 3.12-5.21%.
7. The TiB of claim 12-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that the Cr powder is 2.77-4.61%.
8. The TiB of claim 12-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, characterized in that spark plasma sintering refers to: and (3) placing the dried mixed powder into a mold, heating to the temperature T at the temperature T of 1300-1400 ℃ at the heating rate of 300 ℃/min of 200 ℃/min-300 ℃/min, and preserving the heat for 5-10 minutes in the temperature T environment at the pressure of 50-60 MPa.
9. The TiB of claim 82-Fe-Co-Ni-Cr aluminum liquid corrosion resistant material, characterized in that the heating rate is 200 ℃/min, 250 ℃/min or 300 ℃/min;
t is 1300 ℃, 1350 ℃ or 1400 ℃, and the heat preservation time is 5, 7, 8, 9 or 10 minutes.
10. TiB according to any of claims 1-92-Fe-Co-Ni-Cr aluminium liquid corrosion resistant material, characterized in that the sintering adopts spark plasma sintering.
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JP2005213605A (en) * | 2004-01-30 | 2005-08-11 | Tocalo Co Ltd | Composite material, thermally sprayed film coated member and method for manufacturing the member |
| CN1846006A (en) * | 2003-05-20 | 2006-10-11 | 埃克森美孚研究工程公司 | Advanced erosion-corrosion resistant boride cermets |
-
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| CN1846006A (en) * | 2003-05-20 | 2006-10-11 | 埃克森美孚研究工程公司 | Advanced erosion-corrosion resistant boride cermets |
| JP2005213605A (en) * | 2004-01-30 | 2005-08-11 | Tocalo Co Ltd | Composite material, thermally sprayed film coated member and method for manufacturing the member |
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| CN112626403A (en) * | 2020-12-07 | 2021-04-09 | 湘潭大学 | TiB2-FeCoNiCrMn aluminum liquid corrosion resistant material |
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