阅读说明：本技术 耐铝液腐蚀TiB2-FeCoNiCrMn复合材料的制备方法 (Aluminium liquid corrosion resistant TiB2Preparation method of (E) -FeCoNiCrMn composite material ) 是由 尹付成 高志栋 欧阳雪枚 谢小龙 任可柱 于 2020-12-07 设计创作，主要内容包括：本发明实施例提出了一种耐铝液腐蚀TiB-2-FeCoNiCrMn复合材料的制备方法,所述制备方法包括：按照预设的质量百分比称取TiB-2粉和FeCoNiCrMn粉,并放入球磨机中进行球磨混粉,TiB2粉和FeCoNiCrMn粉的质量百分比的组分构成如下：TiB-2粉70～88％,FeCoNiCrMn粉12～30％；将球磨后的混合粉末放入真空干燥箱中进行干燥；将干燥后的混合粉末放入模具中进行放电等离子烧结,以得到TiB-2-FeCoNiCrMn复合材料。本发明实施例得到的TiB-2-FeCoNiCrMn复合材料具有较高的耐铝液腐蚀性能,且工艺简单,成本低廉,为工业生产提供了切实可靠的制备方法。(The embodiment of the invention provides a molten aluminum corrosion resistant TiB 2 -a method for preparing a FeCoNiCrMn composite, said method comprising: weighing TiB according to preset mass percentage 2 The powder and FeCoNiCrMn powder are put into a ball mill for ball milling and mixing, and the TiB2 powder and the FeCoNiCrMn powder comprise the following components in percentage by mass: TiB 2 70-88% of powder and 12-30% of FeCoNiCrMn powder; putting the mixed powder subjected to ball milling into a vacuum drying box for drying; putting the dried mixed powder into a die for spark plasma sintering to obtain TiB 2 -a FeCoNiCrMn composite. TiB obtained by the embodiment of the invention 2 The FeCoNiCrMn composite material has higher aluminum liquid corrosion resistance, simple process and low cost, and provides a practical and reliable preparation method for industrial production.)

1. Aluminum liquid corrosion resistant TiB₂The preparation method of the FeCoNiCrMn composite material is characterized by comprising the following steps of:

ball milling and powder mixing:

weighing TiB according to preset mass percentage₂Powder and FeCoNiCrMn powder, and putting the powder and FeCoNiCrMn powder into a ball mill for ball milling and mixing, wherein the TiB powder₂The FeCoNiCrMn powder comprises the following components in percentage by mass: the TiB₂70-88% of powder, and 12-30% of FeCoNiCrMn powder;

ball milling and drying:

putting the mixed powder subjected to ball milling into a vacuum drying box for drying;

sintering:

putting the dried mixed powder into a die for spark plasma sintering to obtain TiB₂-a FeCoNiCrMn composite.

2. The molten aluminum corrosion resistant TiB of claim 1₂The preparation method of the FeCoNiCrMn composite material is characterized by further comprising the following steps of:

mechanical alloying step:

weighing Fe powder, Co powder, Ni powder, Cr powder and Mn powder with the same molar ratio, and putting the powder into a ball mill for ball milling;

alloying and drying:

and putting the mixed powder after mechanical alloying into a vacuum drying oven for drying to obtain the FeCoNiCrMn powder.

3. The molten aluminum corrosion resistant TiB of claim 2₂Preparation method of (E) -FeCoNiCrMn composite materialThe method is characterized in that the ball milling in the mechanical alloying step is wet ball milling, absolute ethyl alcohol is used as a control agent in the ball milling process, the ball-material ratio is 5:1, the rotating speed is 200-300 r/min, and the ball milling time is 50-60 h.

4. The molten aluminum corrosion resistant TiB of claim 1₂The preparation method of the FeCoNiCrMn composite material is characterized in that in the step of ball-milling and powder-mixing, the ball-milling and powder-mixing is performed by a wet ball-milling method, absolute ethyl alcohol is used as a ball-milling medium, the ball-material ratio is 3:1, the rotating speed is 150-200 r/min, and the ball-milling time is 2-4 h.

5. The molten aluminum corrosion resistant TiB of claim 2₂The preparation method of the-FeCoNiCrMn composite material is characterized in that the drying temperature in the ball milling drying step and the drying temperature in the alloying drying step are both 70-90 ℃, the vacuum degree is-0.06 MPa-0.1 MPa, and the drying time is 8-12 h.

6. The molten aluminum corrosion resistant TiB of claim 1₂-a method for preparing a FeCoNiCrMn composite, characterized in that in the sintering step: and (3) filling the dried mixed powder into a mold, raising the temperature to a temperature T at a heating rate of 200-300 ℃/min, wherein the temperature T is 1400-1500 ℃, and preserving the heat for 5-10 minutes in the temperature T environment, and the pressure is 50-60 MPa.

7. The molten aluminum corrosion resistant TiB of claim 2₂-FeCoNiCrMn composite material, characterized in that, the TiB₂The purity of the powder is 99.5-99.9%, and the particle size is 2-5 microns; the purity of the Fe powder, the purity of the Co powder, the purity of the Ni powder, the purity of the Cr powder and the purity of the Mn powder are all 99.9-99.99%, and the particle size of the Fe powder, the purity of the Co powder, the purity of the Ni powder, the purity of the Cr powder and the purity of the Mn powder is 5-10 micrometers.

8. The molten aluminum corrosion resistant TiB of claim 2₂-a method for preparing a FeCoNiCrMn composite material, characterized in that said Fe powder, said Co powder, said Ni powder, said Cr powder and said Mn powder are in said same molar ratioThe components by mass percentage are as follows: 19.92% of Fe powder, 21.02% of Co powder, 20.93% of Ni powder, 18.54% of Cr powder and 19.59% of Mn powder.

9. The molten aluminum corrosion resistant TiB of any one of claims 1-7₂-FeCoNiCrMn composite material, characterized in that, the TiB₂The FeCoNiCrMn composite was subjected to a macro-hardness test using a Rockwell hardness tester model HR-150A.

10. The molten aluminum corrosion resistant TiB of any one of claims 1-7₂-FeCoNiCrMn composite material, characterized in that, the TiB₂-said TiB in FeCoNiCrMn composite₂The FeCoNiCrMn powder comprises the following components in percentage by mass: the TiB₂The powder accounts for 80-88%, and the FeCoNiCrMn powder accounts for 12-20%.

Technical Field

The invention relates to the field of aluminum liquid corrosion resistant materials, in particular to an aluminum liquid corrosion resistant TiB₂Of FeCoNiCrMn composite materialsA preparation method.

Background

The earth crust has extremely rich Al content, and the yield of the aluminum and the aluminum alloy is the first of nonferrous metals, so the earth crust is widely applied to the fields of aerospace, traffic, construction, energy and the like. However, in the process of smelting aluminum alloy, the aluminum liquid has extremely strong corrosivity, and can generate chemical reaction with most metals to corrode a metal matrix, in the smelting process, a used crucible, a roller and a shaft sleeve used in the forming of an aluminum product, a sink roller and an aluminum molten pool of hot dip aluminizing in a production line and the like are corroded by the aluminum liquid, in the process of corroding the aluminum liquid, the purity of the aluminum liquid is reduced, corroded materials enter the aluminum liquid to form aluminum slag, the quality of the aluminum product and the quality of a coating are affected, meanwhile, the aluminum liquid corrodes production equipment, the problems of equipment corrosion failure, corrosion perforation of an aluminum liquid containing groove and the like are caused, the production efficiency is reduced, the production cost is increased, and safety accidents can possibly occur in serious cases.

Therefore, the invention provides a preparation method of a molten aluminum corrosion resistant material, which is a problem to be solved urgently.

Disclosure of Invention

The embodiment of the invention discloses a molten aluminum corrosion resistant TiB₂The material prepared by the method has excellent aluminum liquid corrosion resistance, high densification degree and good mechanical property.

Specifically, one embodiment of the invention discloses a molten aluminum corrosion resistant TiB₂The preparation method of the FeCoNiCrMn composite material is characterized by comprising the following steps of:

ball milling and powder mixing:

weighing TiB according to preset mass percentage₂Powder and FeCoNiCrMn powder, and putting the powder and FeCoNiCrMn powder into a ball mill for ball milling and mixing, wherein the TiB powder₂The FeCoNiCrMn powder comprises the following components in percentage by mass: the TiB₂70-88% of powder, and 12-30% of FeCoNiCrMn powder;

ball milling and drying:

putting the mixed powder subjected to ball milling into a vacuum drying box for drying;

sintering:

putting the dried mixed powder into a die for spark plasma sintering to obtain TiB₂-a FeCoNiCrMn composite.

In an embodiment of the present invention, before the step of ball-milling and mixing, the method further includes:

mechanical alloying step:

weighing Fe powder, Co powder, Ni powder, Cr powder and Mn powder with the same molar ratio, and putting the powder into a ball mill for ball milling;

alloying and drying:

and putting the mixed powder after mechanical alloying into a vacuum drying oven for drying to obtain the FeCoNiCrMn powder.

In one embodiment of the invention, the ball milling in the mechanical alloying step is wet ball milling, the ball milling process control agent is absolute ethyl alcohol, the ball-to-material ratio is 5:1, the rotation speed is 200-300 r/min, and the ball milling time is 50-60 h.

In one embodiment of the invention, in the step of ball-milling and powder-mixing, the ball-milling and powder-mixing is performed by a wet ball-milling method, absolute ethyl alcohol is used as a ball-milling medium, the ball-to-material ratio is 3:1, the rotation speed is 150-200 r/min, and the ball-milling time is 2-4 h.

In one embodiment of the invention, the drying temperature in the ball milling drying step and the drying temperature in the alloying drying step are both 70-90 ℃, the vacuum degree is-0.06 MPa-0.1 MPa, and the drying time is 8-12 h.

In one embodiment of the present invention, in the sintering step: and (3) filling the dried mixed powder into a mold, raising the temperature to a temperature T at a heating rate of 200-300 ℃/min, wherein the temperature T is 1400-1500 ℃, and preserving the heat for 5-10 minutes in the temperature T environment, and the pressure is 50-60 MPa.

In one embodiment of the invention, the TiB₂The purity of the powder is 99.5-99.9%, and the particle size is 2-5 microns; the purity of the Fe powder, the purity of the Co powder, the purity of the Ni powder, the purity of the Cr powder and the purity of the Mn powder are all 99.9-99.99%, and the particle size of the Fe powder, the purity of the Co powder, the purity of the Ni powder, the purity of the Cr powder and the purity of the Mn powder is 5-10 micrometers.

In an embodiment of the present invention, the components of the Fe powder, the Co powder, the Ni powder, the Cr powder, and the Mn powder in the same molar ratio in percentage by mass are: 19.92% of Fe powder, 21.02% of Co powder, 20.93% of Ni powder, 18.54% of Cr powder and 19.59% of Mn powder.

In one embodiment of the invention, the TiB₂The FeCoNiCrMn composite was subjected to a macro-hardness test using a Rockwell hardness tester model HR-150A.

In one embodiment of the invention, the TiB₂-said TiB in FeCoNiCrMn composite₂The FeCoNiCrMn powder comprises the following components in percentage by mass: the TiB₂The powder accounts for 80-88%, and the FeCoNiCrMn powder accounts for 12-20%.

The technical scheme has the following advantages or beneficial effects: improvement of TiB by using FeCoNiCrMn high-entropy alloy as binder phase₂Has poor toughness and is not easy to sinter, and can sinter TiB₂The FeCoNiCrMn composite material has extremely high densification degree reaching 94.1-98.6% and excellent aluminum liquid corrosion resistance. In one embodiment of the present invention, TiB is prepared₂The average corrosion rate of the FeCoNiCrMn composite material in aluminum liquid at 700 ℃ is 3.48 multiplied by 10^-4mm/h, 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 and 316L stainless steel in aluminum liquid at 700 ℃ is 1.1 multiplied by 10^-1mm/h, compared with the aluminum liquid corrosion resistance of common cast iron and 316L stainless steel, the TiB of the invention₂TiB obtained by preparation method of-FeCoNiCrMn composite material₂The performance of the FeCoNiCrMn composite material in aluminum liquid corrosion resistance is greatly improved, and the FeCoNiCrMn composite material has good industrial application prospect.

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 description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are only some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on these drawings without creative efforts.

FIG. 1 is a microstructure diagram of FeCoNiCrMn powder according to example 1 of the present invention.

Fig. 2 is an XRD pattern of FeCoNiCrMn powder related to example 1 of the present invention.

FIG. 3 is a microstructure diagram of a mixed powder after ball milling according to example 1 of the present invention.

Fig. 4 is an XRD pattern of the mixed powder after ball milling referred to in example 1 of the present invention.

FIG. 5 shows TiB prepared in example 1 of the present invention₂-microstructural map of FeCoNiCrMn composite.

FIG. 6 shows TiB at two sintering temperatures in examples 1 and 2 of the present invention₂-FeCoNiCrMn composite with TiB₂Hardness profile with increasing content.

FIG. 7 shows TiB in four examples 1-4 of the present invention₂-corrosion depth of FeCoNiCrMn composite as a function of time.

FIG. 8 shows TiB in example 1 of the present invention₂-microstructure of corrosion interface of FeCoNiCrMn composite material after 2, 5, 8, 10, 15 and 20 days of corrosion in aluminum liquid at 700 ℃.

Detailed Description

The technical solutions in the embodiments of the present invention will be clearly and completely described below with reference to the drawings in the embodiments of the present invention, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all of the embodiments. 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.

[ example 1 ]

Aluminum liquid corrosion resistant TiB₂The preparation method of the FeCoNiCrMn composite material comprises the following steps:

(1) sample preparation: mixing TiB₂Fe, Co, Ni, Cr and Mn powder are weighed according to the following mass percent: TiB₂88% of powder, 2.39% of Fe powder, 2.52% of Co powder and 2% of Ni powder.51 percent, Cr powder 2.23 percent and Mn powder 2.35 percent. TiB₂The purity of the powder is 99.8%, the granularity is 3 microns, and the purity of the Fe powder, the Co powder, the Ni powder, the Cr powder and the Mn powder is 99.98%, and the granularity is 6 microns.

(2) Mechanical alloying step: putting Fe powder, Co powder, Ni powder, Cr powder and Mn powder with the same molar ratio into a ball mill such as a ball milling tank, performing wet ball milling, pouring a proper amount of absolute ethyl alcohol, and performing ball milling for 60 hours at a ball-material ratio of 5:1 at a ball mill rotation speed of 300r/min for stopping for half an hour every 4 hours.

(3) Alloying and drying: and (3) drying the mixed powder after mechanical alloying, such as the whole ball milling pot, in a vacuum drying oven for 12 hours at the drying temperature of 90 ℃ and the vacuum degree of below-0.1 MPa to finally obtain the FeCoNiCrMn powder with a single-phase FCC structure. Referring to FIG. 1, a microstructure diagram of FeCoNiCrMn powder is shown, and it can be seen that FeCoNiCrMn high entropy alloy powder with regular shape is obtained. Referring to fig. 2, the XRD pattern of FeCoNiCrMn powder, it can be seen that a single-phase FCC structure has been formed.

(4) Ball milling and powder mixing: FeCoNiCrMn powder and TiB obtained by the alloying and drying steps₂The powder is prepared from 12% FeCoNiCrMn powder and 88% TiB powder by weight percent₂The powders are mixed and in a pellet to pellet ratio of 3:1, for example: 150 grams of balls and 50 grams of the mixed powder were placed in a ball mill jar. 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 4 h.

(5) Ball milling and drying: and (3) putting the mixed powder subjected to ball milling into a vacuum drying oven for drying, wherein the temperature of the drying oven is 90 ℃, the vacuum degree is-0.1 MPa, and the drying time is 12 h. Referring to FIG. 3, a microstructure of the mixed powder after ball milling is shown, and it can be seen that FeCoNiCrMn powder is uniformly distributed in TiB after the ball milling is performed on the mixed powder₂Around the powder, the powder mixing effect is better. Referring to FIG. 4, the XRD pattern of the mixed powder after ball milling shows that the phase of the mixed powder after ball milling is TiB₂And FCCFeCoNiCrMn solid solution, and no phase change occurs in the ball milling process.

(6) Sintering: book (I)The sintering equipment used in the examples was spark plasma sintering, and the dried mixed powder was placed in a cylindrical graphite mold and then sintered in a sintering equipment, and the sintering process was set as follows: the temperature is raised from room temperature to 1500 ℃ at the heating rate of 300 ℃/min, the temperature is kept at 1500 ℃ for 7 minutes, and the pressure is increased by 50-60 MPa in the sintering process. Cooling along with the furnace after sintering is finished, and then demoulding to obtain TiB₂-a FeCoNiCrMn composite. See FIG. 5 for TiB₂Microstructure of FeCoNiCrMn composite under SEM, and TiB in dark gray₂Hard phase, light grey Cr formed during sintering₃B phase, namely a FeCoNiCrMn high-entropy alloy binding phase, a FeCoNiCrMn high-entropy alloy binding phase and a small amount of Cr₃Phase B is distributed in TiB₂Around the hard phase, TiB is filled₂The surrounding void.

(7) Aluminum liquid corrosion resistance test: mixing TiB₂-FeCoNiCrMn composite, TiB obtained in this example₂FeCoNiCrMn composites are sintered cake samples, such as: has a size ofCutting the sample into 5 × 5 × 8mm cuboid samples by using a spark numerical control wire cutting machine, then putting the cuboid samples into a graphite crucible filled with 700 ℃ aluminum liquid for corrosion experiment, heating and preserving heat by using a well type resistance furnace, respectively corroding for 2 days, 5 days, 8 days, 10 days, 15 days and 20 days, and then taking out the cuboid samples, wherein the microstructure diagram of the corrosion interface of the cuboid samples is shown in figure 8, and the 2 days, 5 days, 8 days, 10 days, 15 days and 20 days respectively correspond to figures 8(a) - (f). In the experiment, the depth method is used for measuring the corrosion rate, the corrosion depth and the corrosion rate of the cuboid sample at different times are calculated, and the calculation formula is as follows: v is (a-b)/2t, wherein a is the thickness of the cuboid sample before corrosion, b is the thickness of the cuboid sample after corrosion, and t is corrosion time, the thickness a of the cuboid sample before corrosion is accurately measured by a micrometer before a corrosion experiment, then the tissue observation is carried out on the complete cross section of the cuboid sample after corrosion under a scanning electron microscope, and the residual thickness b of the cuboid sample after corrosion is measured by SmileView software. Calculating the average corrosion rate of the cuboid sample to be 3.48 multiplied by 10 according to the corrosion days^-4mm/h. The invention performs a macroscopic hardness test on a cuboid sample by using a Rockwell hardness tester HR-150A. Therein, test TiB₂The macro hardness of the FeCoNiCrMn composite is 74.36 HRC.

In the experiment, it is easy to find that the molten aluminum is applied to TiB through cuboid samples with different corrosion days shown in FIGS. 8(a) - (f)₂The FeCoNiCrMn composite material is corroded, but a corrosion layer is not separated from a matrix, and the aluminum liquid is prevented from further corroding the matrix, so that the corrosion rate is reduced, the material still keeps the original form, a practical and reliable preparation technology is provided for the preparation of the aluminum liquid corrosion resistant material, and the FeCoNiCrMn composite material has high application value during preparation and production.

[ example 2 ]

Compared with the method of example 1, the method of example 2 is the same except that the step (6), i.e., the sintering step, is different, and is not described herein again. Step (6) sintering step of example 2: 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 ℃ at a heating rate of 300 ℃/min, preserving heat at 1400 ℃ for 7 minutes, and pressurizing at 50-60 MPa in the sintering process. Cooling along with the furnace after sintering is finished, and then demoulding to obtain TiB₂-FeCoNiCrMn composite material, calculating TiB obtained in example 2 according to the formula₂-the corrosion rate of the FeCoNiCrMn composite material is 5.79 x 10^-4mm/h, TiB test using a Rockwell hardness tester model HR-150A₂The macro hardness of the FeCoNiCrMn composite is 69.32 HRC.

Wherein, referring to FIG. 6, TiB is obtained at two different sintering temperatures in example 1 and example 2₂-FeCoNiCrMn composite with TiB₂Hardness profile of mass percent increase, TiB₂TiB in FeCoNiCrMn composite material₂In the range of 70 to 88% by mass, TiB₂The hardness of the FeCoNiCrMn composite material can follow that of TiB₂Increase of the content inThe hardness at 1500 ℃ is higher than that at 1400 ℃ and the hardness at 1500 ℃ is higher, and in TiB₂At a content of 80%, the difference in hardness between the two temperatures is greatest at TiB₂At a content of 70%, TiB at two temperatures₂The hardness difference of the FeCoNiCrMn composite material is minimum, and the FeCoNiCrMn composite material has higher reference significance in actual preparation and production based on the characteristics.

[ example 3 ]

Compared with the method in example 2, the method in example 3 is the same except that the step (1), i.e., the sample preparation step, is different, and is not described herein again. Step 1 in example 3 is the sample preparation step: mixing TiB₂Fe, Co, Ni, Cr and Mn powder are weighed according to the following mass percent: TiB₂80% of powder, 3.98% of Fe powder, 4.20% of Co powder, 4.19% of Ni powder, 3.71% of Cr powder and 3.92% of Mn powder. TiB₂The purity of the powder is 99.5%, the granularity is 5 microns, and the purity of the Fe powder, the Co powder, the Ni powder, the Cr powder and the Mn powder is 99.9%, and the granularity is 10 microns. TiB obtained in example 3 was calculated according to the formula₂-FeCoNiCrMn composite material having a corrosion rate of 5.70X 10^-3mm/h, the TiB obtained in example 3 was tested using a Rockwell hardness tester type HR-150A₂The macroscopic hardness of the FeCoNiCrMn composite is 54.61 HRC.

[ example 4 ]

Compared with the method in example 1, the method in example 4 is the same except that the step (1), i.e., the sample preparation step, is different, and is not described herein again. Sample preparation step of step 1 in example 4: mixing TiB₂Fe, Co, Ni, Cr and Mn powder are weighed according to the following mass percent: TiB₂70% of powder, 5.98% of Fe powder, 6.30% of Co powder, 6.28% of Ni powder, 5.56% of Cr powder and 5.88% of Mn powder. TiB₂The purity of the powder was 99.5% and the particle size was 5 microns. The purity of Fe powder, Co powder, Ni powder, Cr powder and Mn powder is 99.9%, and the granularity is 10 microns. TiB obtained in example 4 was calculated₂-FeCoNiCrMn composite material having corrosion rate of 6.31X 10^-3mm/h. TiB obtained in example 4 was tested using a Rockwell hardness tester type HR-150A₂The macroscopic hardness of the FeCoNiCrMn composite is 51.24 HRC.

In summary, referring to FIG. 7, TiB obtained in examples 1-4, respectively₂-corrosion depth of FeCoNiCrMn composite as a function of time. As can be seen, the TiB is in the same species as the corrosion time is prolonged₂Content of TiB₂In the samples of FeCoNiCrMn composite materials, such as the samples of example 1 and example 2, compared with the sample of example 2, the sintering temperature is the highest in the sample of example 1, and TiB obtained in the sample of example 1₂The FeCoNiCrMn composite material has the best aluminum liquid corrosion resistance. Example 1 compared to example 4, containing 88% TiB at the same sintering temperature of 1500 deg.C₂Of TiB₂Sample ratios of FeCoNiCrMn composite containing 70% TiB₂Of TiB₂The sample of the FeCoNiCrMn composite material has better aluminum liquid corrosion resistance. Example 2 compared to example 3 at the same sintering temperature of 1400 deg.C, contained 88% TiB₂Of TiB₂Sample ratios of FeCoNiCrMn composite containing 80% TiB₂Of TiB₂The sample of the FeCoNiCrMn composite material has better aluminum liquid corrosion resistance. According to the calculated TiB obtained in example 1₂The average corrosion rate of the FeCoNiCrMn composite is: 3.48X 10^-4mm/h, TiB in example 2₂The average corrosion rate of the FeCoNiCrMn composite is: 5.79X 10^-4mm/h, TiB in example 3₂The average corrosion rate of the FeCoNiCrMn composite is: 5.70X 10^-3mm/h and TiB in example 4₂The average corrosion rate of the FeCoNiCrMn composite material is 6.31X 10^-3mm/h, compared with the corrosion rate of cast iron in molten aluminum of 0.85mm/h, the TiB of the invention₂The FeCoNiCrMn composite material has absolute advantage in aluminum corrosion resistance rate, and the aluminum liquid corrosion resistance is greatly improved.

In addition, it should be understood that the foregoing embodiments are merely exemplary illustrations of the present invention, and the technical solutions of the embodiments can be arbitrarily combined and collocated without conflict between technical features and structural contradictions, which do not violate the purpose of the present invention.

Finally, it should be noted that: the above examples are only intended to illustrate the technical solution of the present invention, but not to limit it; although the present invention has been described in detail with reference to the foregoing embodiments, it will be understood by those of ordinary skill in the art that: the technical solutions described in the foregoing embodiments may still be modified, or some technical features may be equivalently replaced; and such modifications or substitutions do not depart from the spirit and scope of the corresponding technical solutions of the embodiments of the present invention.