Performance of TiB 2 Wettable Cathode Coating

: A TiB 2 wettable cathode coating was deposited on a graphite carbon cathode material via atmospheric plasma spraying (APS). The microstructure and phase composition of the TiB 2 coating were analyzed via scanning electron microscopy (SEM), X-ray diffraction (XRD), and energy-dispersive X-ray spectroscopy (EDS). The wettability and corrosion resistance of the coating were studied in a molten-aluminum electrolytic system. The results showed that the surface of the TiB 2 coating prepared via plasma spraying was ﬂat and that the main phase of the coating was TiB 2 . The wettability between the TiB 2 coating and liquid aluminum was better than that between graphite cathode carbon block and liquid aluminum. The abilities of the TiB 2 coating and graphite cathode carbon block to resist sodium (Na) penetration and prevent molten salt corrosion were compared through a corrosion test. The TiB 2 coating was found to have better resistance to Na penetration and better refractory cryolite corrosion resistance than graphite cathode carbon block.


Introduction
Currently, cryolite molten salt electrolysis is the only method for smelting aluminum [1]. During the electrolysis of molten cryolite, the cathode carbon block exhibits some corrosion properties; especially, sodium (Na) permeates into the cathode carbon block and causes the expansion of the carbon block, which is the main cause of the cathode damage and failure [2].
In recent years, our research group has conducted numerous studies on the TiB 2 coating preparation via atmospheric plasma spraying (APS) and has achieved certain results. Through several orthogonal experiments on spraying parameters, the best process conditions for the coating preparation have been obtained [16]. The influence of mechanical properties has been studied [17]. The current study mainly investigates the microstructure of TiB 2 coating prepared via APS under optimal process conditions and the wettability and corrosion resistance of TiB 2 coating in a molten-salt electrolytic aluminum system.

Materials
The TiB 2 powder used in the experiment was obtained from a certain chemical industry research institute in Shenyang (TiB 2 ≥ 98.5%), with a particle size of −325-+400 mesh (38-45 µm). For aluminum electrolysis, a graphite cathode carbon block was adopted as the matrix (the specification was 100 mm × 100 mm × 30 mm); it was provided by an aluminum factory in Yunnan and needed to be polished and sandblasted in advance.

Preparation of Plasma-Sprayed TiB 2 Coating
During the TiB 2 coating preparation, first, the carbon block and TiB 2 powder were placed into the drying box and heated up to 100 • C for 4 h to remove the moisture, improve the TiB 2 powder fluidity, and improve the bonding strength between the carbon block and TiB 2 coating. Furthermore, TiB 2 powder was deposited on the graphite cathode carbon block using the DH-2080 plasma spray gun(Shanghai Ruifa Spraying Machinery Co., Ltd., Shanghai, China), with argon as the main gas, hydrogen as the secondary gas, and argon and hydrogen as the powder carrier gases. Before the preparation of the TiB 2 wettable cathode coating via spraying, the DH-2080 plasma spray gun was used to preheat the surface of the roughened and clean carbon block. The preheating temperature was maintained between 100 • C and 200 • C to shorten the temperature difference between the substrate and the TiB 2 powder and reduce the residual stress between the coating and the carbon block substrate. After the preheating, the plasma-spraying process parameters (Table 1) were adjusted, and the TiB 2 coating was sprayed on the carbon block substrate to obtain a TiB 2 coating with~1000 µm thickness.

TiB 2 Coating Characterization
The TiB 2 coating prepared via plasma spraying was peeled off from the base carbon block and then ground. The phase composition of the prepared TiB 2 coating powder was analyzed using the X'pert 3 powder-type diffractometer produced by PANalytical (Malvern, UK). The parameters were as follows: Cu target, acceleration voltage of 40 kV, current of 40 mA, and sweep speed of 8 • min −1 . After the TiB 2 cathode coating subjected to different treatments was polished with sandpaper, the coating surface was observed under a QUANTA600 scanning electron microscope to detect the microscopic internal structure of the coating. Moreover, energy spectrum analysis was performed using the NORAN SYSTEM SIX energy spectrometer (SelectScience, Bath, UK).

Method for Wettability Measurement
In this study, the wetting angle between the plasma-sprayed TiB 2 inert cathode coating and molten aluminum was not directly measured; only the wettability between the TiB 2 inert cathode coating and molten aluminum was qualitatively characterized. First, an appropriate number of aluminum ingots were placed in the silicon carbide crucible, and the silicon carbide crucible was placed in a resistance furnace, model RF-15-10, produced by Changsha Gongtai Experimental Electric Furnace Co., Ltd (Changsha, China), and the heating system was set to 750 • C. When the aluminum ingot in the silicon carbide crucible became molten, the plasma-sprayed TiB 2 cathode coating sample and the aluminum electrolytic cathode carbon block preheated at the same temperature were simultaneously immersed in the molten aluminum; the immersion time was 5 s. Subsequently, the sample was taken out from the molten aluminum and placed on a steel plate at 45 • C with the horizontal ground. After the molten aluminum on the surface of the sample was cooled, aluminum was found to occur on the TiB 2 inert cathode coating and the carbon block. The spreading situations on the cathode and the wettability of the TiB 2 coating and carbon block were qualitatively evaluated.

Corrosion Resistance Test Method
Determination of the dissolution loss of TiB 2 coating in molten aluminum: The TiB 2 coating sample was soaked in high-temperature liquid aluminum at 960 • C for 48 h. After the molten aluminum sample was cooled, the change in the Ti content in the molten aluminum was analyzed, and then the dissolution loss of the TiB 2 coating in the molten aluminum was evaluated. The ARL841OX XRF was used to determine the titanium content in the liquid aluminum.
Static molten salt corrosion test of TiB 2 coating: The TiB 2 coating sample was placed on the bottom of a 0.5 L graphite crucible, and the prepared electrolyte (including Na 3 AlF 6 , NaF, Al 2 O 3 , and CaF 2 in mass percentages of 71.5%, 14.5%, 9.0%, and 5.0%, respectively) was added into a graphite crucible. The crucible was placed into a 960 • C atmosphere furnace and kept for 100 h. After the corrosion was over, the crucible was cooled to room temperature. Then, the TiB 2 coating sample at the bottom of the electrolytic cell was removed, and the residual electrolyte on the surface was cleaned. The sample was then cut along the central axis. Scanning electron microscopy (SEM) and energy-dispersive X-ray spectroscopy (EDS) were used to characterize the TiB 2 coating after static corrosion.
Static molten salt corrosion test of TiB 2 coating: The TiB 2 coating sample was placed on the bottom of a 0.5 L graphite crucible, and the prepared electrolyte (including Na 3 AlF 6 , NaF, Al 2 O 3 , and CaF 2 in mass percentages of 71.5%, 14.5%, 9.0%, and 5.0%, respectively) was added into the graphite crucible. The crucible was then placed into a 980 • C pit furnace. The graphite anode embedded in cast iron was inserted into the electrolytic cell. The area of the graphite anode was 28 cm 2 . After the electrolyte was melted, the current density was kept at 0.7 A·cm −2 , and electrolysis was conducted for 4 h. The electrolyte was added to the electrolytic cell every 15 min. The subsequent treatment after electrolysis was the same as that in the static test. Figure 1a,b are the SEM images of the TiB 2 coating surface prepared via APS at two different magnifications. Figure 1a shows that the coating internal structure was relatively dense and uniformly distributed. The coating mainly showed two colors of dark gray and white. Moreover, small cracks occurred in the coating. The formation of such microcracks depends on the melting of TiB 2 , the volume shrinkage of the particles, and the TiB 2 coating cooling process. Figure 1b shows that after the TiB 2 powder was remelted and recrystallized, the particle size of the coating was not uniform. The distribution of such particles led to the generation of pores in the coating, and the increase in porosity will reduce the coating hardness and the bonding strength between the coating and the substrate; moreover, it will destroy the conductive network of the TiB 2 coating and increase the coating resistivity. Figure 2a,b are the cross-sectional topography images of the TiB 2 coating under two different magnifications. The figure shows a clear boundary between the substrate and the coating. The gray area is the TiB 2 coating, and the black area is the carbon block substrate. The coating was formed by injecting TiB 2 powder into a high-temperature plasma jet and then transporting it to the substrate. The temperature at the center of the plasma flame was as high as 32,000 K, and the temperature at the nozzle outlet was still up to 20,000 K. The TiB 2 powder particles were instantly heated to a molten or semi-melted state in the high-temperature plasma jet. When the particles hit the carbon block substrate surface, they spread into a flat liquid covering and clung to the concave and convex points on the surface of the carbon block substrate. It shrank and bit the anchor point during condensation. Therefore, the combination of the TiB 2 coating and the carbon block substrate was mainly mechanical embedded-type. Because the TiB 2 coating was formed by solidifying a single Minerals 2022, 12, 27 4 of 11 particle as a unit to the substrate surface in a layered accumulation, the difference in particle size between the droplets resulted in some voids in the coating. Moreover, it can be seen from the cross section of the coating that the substrate and the coating. The bonding interface of the layer was clear, smooth, and tortuous, which shows that the coating was tightly bonded.  The gray area is the TiB2 coating, and the black area is the carbon block substrate. The coating was formed by injecting TiB2 powder into a high-temperature plasma jet and then transporting it to the substrate. The temperature at the center of the plasma flame was as high as 32,000 K, and the temperature at the nozzle outlet was still up to 20,000 K. The TiB2 powder particles were instantly heated to a molten or semi-melted state in the high-temperature plasma jet. When the particles hit the carbon block substrate surface, they spread into a flat liquid covering and clung to the concave and convex points on the surface of the carbon block substrate. It shrank and bit the anchor point during condensation. Therefore, the combination of the TiB2 coating and the carbon block substrate was mainly mechanical embedded-type. Because the TiB2 coating was formed by solidifying a single particle as a unit to the substrate surface in a layered accumulation, the difference in particle size between the droplets resulted in some voids in the coating. Moreover, it can be seen from the cross section of the coating that the substrate and the coating. The bonding interface of the layer was clear, smooth, and tortuous, which shows that the coating was tightly bonded.   The gray area is the TiB2 coating, and the black area is the carbon block substrate. The coating was formed by injecting TiB2 powder into a high-temperature plasma jet and then transporting it to the substrate. The temperature at the center of the plasma flame was as high as 32,000 K, and the temperature at the nozzle outlet was still up to 20,000 K. The TiB2 powder particles were instantly heated to a molten or semi-melted state in the high-temperature plasma jet. When the particles hit the carbon block substrate surface, they spread into a flat liquid covering and clung to the concave and convex points on the surface of the carbon block substrate. It shrank and bit the anchor point during condensation. Therefore, the combination of the TiB2 coating and the carbon block substrate was mainly mechanical embedded-type. Because the TiB2 coating was formed by solidifying a single particle as a unit to the substrate surface in a layered accumulation, the difference in particle size between the droplets resulted in some voids in the coating. Moreover, it can be seen from the cross section of the coating that the substrate and the coating. The bonding interface of the layer was clear, smooth, and tortuous, which shows that the coating was tightly bonded.  Figure 3 is the X-ray diffraction (XRD) analysis result of the TiB2 coating prepared via APS. The figure shows that the coating was mainly composed of TiB2, TiO2, and a small amount of B2O3, indicating that TiB2 was oxidized during the spraying process. This was mainly due to the air involved in the plasma jet and the molten TiB2 particles during the  Figure 3 is the X-ray diffraction (XRD) analysis result of the TiB 2 coating prepared via APS. The figure shows that the coating was mainly composed of TiB 2 , TiO 2 , and a small amount of B 2 O 3 , indicating that TiB 2 was oxidized during the spraying process. This was mainly due to the air involved in the plasma jet and the molten TiB 2 particles during the plasma-spraying process. Contact causes TiB 2 particles to be oxidized to form oxidation products such as TiO 2 and B 2 O 3 .

X-ray Diffraction Pattern of TiB 2 Coating
plasma-spraying process. Contact causes TiB2 particles to be oxidized to form oxidation products such as TiO2 and B2O3.  Figure 4 compares the peeling of molten aluminum from two samples. Figure 4c shows that the liquid aluminum spreading on the surface of the carbon block cathode was easily peeled off from the substrate and will not peel off with the carbon block material. Figure 4d shows that it is desired to spread the It is very difficult for the liquid aluminum on the surface of the layer to peel off from the TiB2 substrate. The adhesion of the liquid aluminum to the coating is strong, and during the peeling of the coating, part of the coating materials peel off with the substrate; this also shows that the coating prepared by TiB2 inert cathode in this study has good wettability.   Figure 4 compares the peeling of molten aluminum from two samples. Figure 4c shows that the liquid aluminum spreading on the surface of the carbon block cathode was easily peeled off from the substrate and will not peel off with the carbon block material. Figure 4d shows that it is desired to spread the It is very difficult for the liquid aluminum on the surface of the layer to peel off from the TiB 2 substrate. The adhesion of the liquid aluminum to the coating is strong, and during the peeling of the coating, part of the coating materials peel off with the substrate; this also shows that the coating prepared by TiB 2 inert cathode in this study has good wettability. plasma-spraying process. Contact causes TiB2 particles to be oxidized to form oxidation products such as TiO2 and B2O3.  Figure 4 compares the peeling of molten aluminum from two samples. Figure 4c shows that the liquid aluminum spreading on the surface of the carbon block cathode was easily peeled off from the substrate and will not peel off with the carbon block material. Figure 4d shows that it is desired to spread the It is very difficult for the liquid aluminum on the surface of the layer to peel off from the TiB2 substrate. The adhesion of the liquid aluminum to the coating is strong, and during the peeling of the coating, part of the coating materials peel off with the substrate; this also shows that the coating prepared by TiB2 inert cathode in this study has good wettability.   Figure 5 depicts the change curve of the TiB 2 coating prepared via plasma spraying in molten aluminum. The figure shows that the quality of the TiB 2 coating remained unchanged and basically stable within 48 h of corrosion in high-temperature molten aluminum, demonstrating a good resistance to corrosion by molten aluminum. This is mainly because the TiB 2 material had good wettability to liquid aluminum and low solubility in liquid aluminum. Moreover, the TiB 2 coating prepared via plasma spraying was uniform and dense, demonstrating the good resistance of the TiB 2 material to liquid aluminum erosion.  Figure 5 depicts the change curve of the TiB2 coating prepared via plasma spraying in molten aluminum. The figure shows that the quality of the TiB2 coating remained unchanged and basically stable within 48 h of corrosion in high-temperature molten aluminum, demonstrating a good resistance to corrosion by molten aluminum. This is mainly because the TiB2 material had good wettability to liquid aluminum and low solubility in liquid aluminum. Moreover, the TiB2 coating prepared via plasma spraying was uniform and dense, demonstrating the good resistance of the TiB2 material to liquid aluminum erosion. According to the XRD analysis, after the TiB2 coating was corroded in high-temperature liquid aluminum (960 °C) for 120 min, no Ti component was detected, and the main component in the liquid aluminum was Al ( Figure 6). The TiB2 coating prepared via plasma spraying could be well wetted by molten aluminum and had excellent corrosion resistance to molten aluminum. Moreover, the elemental analysis method was used to detect the Ti content in the molten aluminum. The Ti content of the molten aluminum was 0.0042%, which was only 0.0016% higher than that of the original aluminum (0.0026%). It was found that the titanium content in the original aluminum was 0.0026% (mass percent), and after the TiB2 coating was immersed in the aluminum solution for 48 h, the titanium content in the analyzed aluminum was 0.0042% (mass percent), which was only 0.0016% higher than the original aluminum content of 0.0026%. According to this calculation, the industrial tank was coated with 1 mm. The service life of thick pure TiB2 coating should be over four years. According to the XRD analysis, after the TiB 2 coating was corroded in high-temperature liquid aluminum (960 • C) for 120 min, no Ti component was detected, and the main component in the liquid aluminum was Al ( Figure 6). The TiB 2 coating prepared via plasma spraying could be well wetted by molten aluminum and had excellent corrosion resistance to molten aluminum. Moreover, the elemental analysis method was used to detect the Ti content in the molten aluminum. The Ti content of the molten aluminum was 0.0042%, which was only 0.0016% higher than that of the original aluminum (0.0026%). It was found that the titanium content in the original aluminum was 0.0026% (mass percent), and after the TiB 2 coating was immersed in the aluminum solution for 48 h, the titanium content in the analyzed aluminum was 0.0042% (mass percent), which was only 0.0016% higher than the original aluminum content of 0.0026%. According to this calculation, the industrial tank was coated with 1 mm. The service life of thick pure TiB 2 coating should be over four years.

Analysis of Static Corrosion Results of TiB 2 Coating
Resistance to Na penetration is an important indicator of wettable cathode materials. Figure 7a is a low-power-SEM image of the surface of the sample after the static corrosion of the carbon block, and Figure 7b is a low-power-SEM image of the TiB 2 coating surface after static corrosion. The figure shows that after cryolite corrosion under the same conditions, the surface of the carbon block cathode was loose and porous, the area of the carbon block was significantly reduced, and the electrolyte was more likely to penetrate into the carbon block. Figure 8a is the surface micro-topography image of the TiB 2 coating after corrosion, and Figure 8b is the cross-sectional micro-topography image of the TiB 2 coating after corrosion. Figure 8a shows that after the coating surface was corroded, the TiB 2 particles still maintained the original crystal structure state and were not corroded by cryolite melt.  Figure 8b shows that the TiB 2 coating cross section also maintained the original complete structure; the coating structure was still dense. After 100 h of static corrosion, the TiB 2 coating internal structure was dense, and the corrosion resistance was good. Figure 9 shows the EDS spectrum of the TiB 2 coating after corrosion. The figure shows that the main component element in the coating was Ti, and the metal Na + ions did not penetrate into the coating.

Analysis of Static Corrosion Results of TiB2 Coating
Resistance to Na penetration is an important indicator of wettable cathode materials. Figure 7a is a low-power-SEM image of the surface of the sample after the static corrosion of the carbon block, and Figure 7b is a low-power-SEM image of the TiB2 coating surface after static corrosion. The figure shows that after cryolite corrosion under the same conditions, the surface of the carbon block cathode was loose and porous, the area of the carbon block was significantly reduced, and the electrolyte was more likely to penetrate into the carbon block. Figure 8a is the surface micro-topography image of the TiB2 coating after corrosion, and Figure 8b is the cross-sectional micro-topography image of the TiB2 coating after corrosion. Figure 8a shows that after the coating surface was corroded, the TiB2 particles still maintained the original crystal structure state and were not corroded by cryolite melt. Figure 8b shows that the TiB2 coating cross section also maintained the original complete structure; the coating structure was still dense. After 100 h of static corrosion, the TiB2 coating internal structure was dense, and the corrosion resistance was good. Figure  9 shows the EDS spectrum of the TiB2 coating after corrosion. The figure shows that the main component element in the coating was Ti, and the metal Na + ions did not penetrate into the coating.

Analysis of Static Corrosion Results of TiB2 Coating
Resistance to Na penetration is an important indicator of wettable cathode materials. Figure 7a is a low-power-SEM image of the surface of the sample after the static corrosion of the carbon block, and Figure 7b is a low-power-SEM image of the TiB2 coating surface after static corrosion. The figure shows that after cryolite corrosion under the same conditions, the surface of the carbon block cathode was loose and porous, the area of the carbon block was significantly reduced, and the electrolyte was more likely to penetrate into the carbon block. Figure 8a is the surface micro-topography image of the TiB2 coating after corrosion, and Figure 8b is the cross-sectional micro-topography image of the TiB2 coating after corrosion. Figure 8a shows that after the coating surface was corroded, the TiB2 particles still maintained the original crystal structure state and were not corroded by cryolite melt. Figure 8b shows that the TiB2 coating cross section also maintained the original complete structure; the coating structure was still dense. After 100 h of static corrosion, the TiB2 coating internal structure was dense, and the corrosion resistance was good. Figure  9 shows the EDS spectrum of the TiB2 coating after corrosion. The figure shows that the main component element in the coating was Ti, and the metal Na + ions did not penetrate into the coating.     Figure 10 is a cross-sectional view of the TiB2 coating after dynamic corrosion, and Figure 11 is the cross section of the TiB2 coating after the dynamic corrosion experiment and the EDS energy spectrum of points taken near the TiB2 coating surface.   Figure 10 is a cross-sectional view of the TiB 2 coating after dynamic corrosion, and Figure 11 is the cross section of the TiB 2 coating after the dynamic corrosion experiment and the EDS energy spectrum of points taken near the TiB 2 coating surface.   Figure 10 is a cross-sectional view of the TiB2 coating after dynamic corrosion, and Figure 11 is the cross section of the TiB2 coating after the dynamic corrosion experiment and the EDS energy spectrum of points taken near the TiB2 coating surface.  Figure 10a shows that the TiB2 coating after electrolysis maintained a compact structure. Figure 10b shows that the bonding surfaces of the TiB2 coating and the carbon block substrate were in good contact, without peeling or porosity of the coating. The TiB2 coating had good bonding strength with the carbon block substrate. From the analysis of the EDS results, a small amount of cryolite components such as F, Na, Al, and Ca occurred in Figure 11. Cross section and EDS spectrum of coating after corrosion. Figure 10a shows that the TiB 2 coating after electrolysis maintained a compact structure. Figure 10b shows that the bonding surfaces of the TiB 2 coating and the carbon block substrate were in good contact, without peeling or porosity of the coating. The TiB 2 coating had good bonding strength with the carbon block substrate. From the analysis of the EDS results, a small amount of cryolite components such as F, Na, Al, and Ca occurred in this area. The main component of the coating was Ti; this indicates that a small amount of cryolite penetrated the coating surface after the electrolysis experiment; the penetration depth was not deep, indicating that the TiB 2 coating obtained via plasma spraying has improved resistance to cryolite corrosion. The TiB 2 wettable cathode coating prepared through plasma spraying technology does not contain carbon elements, which avoids the defect that the TiB 2 /C carbon glue coating is easily corroded by the electrolyte due to carbon elements.

Conclusions
In this study, under optimal parameters and the optimal particle size, a TiB 2 coating was prepared on a carbon cathode surface using plasma-spraying equipment, and the phase and microstructure of the coating were analyzed via SEM, XRD, and other characterization methods. After the analysis, the wettability and corrosion resistance of the coating were measured, and the following conclusions were drawn: The TiB 2 coating prepared via APS had a smooth surface free of peeling and cracking. The TiB 2 coating internal structure was dense and uniform. The large particles were in a semi-melted state, forming a disc-shaped structure embedded in the coating, and the small particles were completely melted; they connected the large particles to fill the pores between the large particles. In the plasma-spraying process, the air drawn into the plasma jet contacted the molten TiB 2 particles, causing the TiB 2 particles to be oxidized and form oxidation products such as TiO 2 and B 2 O 3 . TiB 2 is still the most important phase component in the coating.
The wettability between the TiB 2 wettable cathode coating and molten aluminum was significantly better than that between graphite cathode carbon block and molten aluminum. Through static corrosion experiments, the abilities of the TiB 2 coating and graphite cathode carbon block to resist Na penetration and to prevent molten cryolite corrosion were compared. The TiB 2 coating resistance to Na penetration and corrosion resistance to molten cryolite were better than those of the graphite cathode carbon block. Moreover, after the TiB 2 coating was dynamically corroded for 4 h, only a small amount of F, Na, and Al penetrated into the TiB 2 coating inner surface. Given the results, the TiB 2 coating prepared via plasma spraying has good liquid aluminum wetting ability and good resistance to Na penetration.

Future Prospective
The oxidation behavior of TiB2 in the plasma spraying process is very complex, the process is very much influenced by the transfer (momentum transfer, heat transfer and mass transfer), especially the transfer phenomenon of gas phase B2O3 under high temperature conditions determines the TiB2 oxidation behavior, and the plasma spraying TiB2 coating is carried out under high temperature conditions, and metallurgical bonding is observed through experiments, however, the bonding mechanism and the effect on TiB2 coating properties are still unclear; finally the introduction of multi-component TiB2 base can further improve the properties of the coating such as corrosion resistance and wettability. Therefore, on the basis of this thesis study, the following studies are proposed to be carried out in the future: (1) Study the momentum transfer, heat transfer and mass transfer behaviors of TiB2 during the movement to the surface of carbon block during the spraying process, analyze the time-varying laws of flow field and temperature field, and reveal the oxidation behavior of TiB2 and the symmetry mechanism of multi-physical field; and study in depth the mechanism of pore formation of TiB2 coating under high temperature conditions and study the transfer phenomenon of gas phase B2O3. (2) To study the metallurgical bonding behavior of TiB2 coating process for electrolytic aluminum by plasma spraying, to study the generation of new substances and formation of new chemical bonds by quantum chemical methods, and to reveal the possible chemical reactions by searching for transition states, and to propose the mechanism of the influence of metallurgical bonding on the performance of TiB2 coating through the study. (3) On the basis of TiB2 coating research, we study multi-component TiB2 based coating materials for aluminum electrolysis, add rare earth group elements to TiB2 raw materials, study the mechanism of its addition on the performance of coating materials, and explore new high-performance TiB2-based coating materials for aluminum electrolysis. Funding: This research received no external funding.
Data Availability Statement: Data sharing not applicable. No new data were created or analyzed in this study. Data sharing is not applicable to this article.