Oxidation Resistance of Double-Layer MoSi2–Borosilicate Glass Coating on Fiber-Reinforced C/SiO2 Aerogel Composite

An MoSi₂–borosilicate glass coating with high emissivity and oxidation resistance was prepared on the surface of the fiber-reinforced C/SiO₂ aerogel composite by the slurry method combined with the embedding sintering method under the micro-oxygen atmosphere. The microstructure and phase composition of the coatings with different MoSi₂ contents before and after static oxidation were investigated. This composite material has both excellent radiating properties and outstanding oxidation resistance. The total emissivity values of the as-prepared coatings are all above 0.8450 in the wavelength of 300∼2,500 nm. Meanwhile, the as-prepared M40 coating also has superior thermal endurance after the isothermal oxidation of 1,200°C for 180 min with only 0.27% weight loss, which contributes to the appropriate viscosity of the binder to relieve thermal stress defects. This material has broad application prospects in thermal protection.

Introduction

With the development of hypersonic aircraft and spacecraft, the external surfaces of vehicles experience an intense aerodynamic heating load, which will lead to the failure of internal structures (Levchenko et al., 2018). Therefore, the vehicles must be protected by a lightweight and stable thermal protection, which possesses high emissivity, anti-oxidation coating, and low thermal conductivity insulation (Shao et al., 2019). For spacecraft, thermal radiation is considered to be the most important way to dissipate heat, while thermal conduction and thermal convection are negligible under a vacuum environment (Sun et al., 2017). Thus, high emissivity coating has drawn more and more attention in the aerospace thermal protection system. The substrate material plays a vital role in this system including mechanical load-bearing, anti-erosion, and further isolated heat. Therefore, the choice of the substrate directly affects the efficient and stable service of the thermal protection system. At present, the thermal insulation materials for thermal protection systems mostly focus on high-temperature ceramic matrix composites (Cui et al., 2018; Savino et al., 2018; Grigoriev et al., 2020; Sun et al., 2021), carbon/carbon composites (Paul et al., 2017; Du et al., 2018a; Liu et al., 2019; Li et al., 2020a), etc. These thermal insulation materials function to protect the internal structure of aircraft, which also exhibit deficiencies such as high thermal conductivity, insufficient temperature resistance, and high brittleness. To meet the requirements of complex space environments, it is of great significance to develop a new thermal insulation material with low thermal conductivity, low density, excellent temperature resistance, and high mechanical strength.

Aerogel, a kind of nano-porous material, exhibits excellent properties such as low density (Zhu et al., 2020), high specific area (Wu et al., 2017), high porosity (Li et al., 2019a; Zhao et al., 2020), and low thermal conductivity (Su et al., 2020), which receives great attention, becoming one of the most potential materials for the high-temperature thermal insulator in a thermal protection system. However, traditional SiO₂ aerogel cannot maintain its thermal stability in the long-time working temperature exceeding 800°C (Cai et al., 2020). Though Al₂O₃ aerogel shows improved thermal resistance, the metastable alumina phase converts to stable α-Al₂O₃ after temperature over 1,050°C and contributes to the collapse of the nano-porous structure and a considerable loss of surface area (Yang et al., 2020). Compared with SiO₂ aerogel and Al₂O₃ aerogel, carbon aerogel has the highest thermal stability and can maintain a mesoporous structure even over 2000°C in an inert atmosphere (Lee and Park, 2020). However, carbon aerogel has insufficient mechanical strength, which is fragile and easily collapses (Li et al., 2019b). Reinforcing the carbon-based aerogel with fibers is an effective way to overcome the problems of brittleness and liner shrinkage (Feng et al., 2011). Moreover, carbon aerogel will be oxidized above 500°C in an aerobic environment. Therefore, high emissivity and anti-oxidation coating are essential for carbon-based aerogel (Li et al., 2019b), which can protect the substrate from oxygen erosion and plays the role of radiating surface heat.

Generally, high emissivity and anti-oxidation coating are mainly composed of the radiation agent (Du et al., 2018b) and binder agent (Shao et al., 2017a). The radiation agent plays the role of absorbing and reradiating thermal energy. And the binder agent, which is generally of the amorphous phase, can connect with the substrate and adjust the thermal expansion coefficient and improve the antioxidant performance. The intermetallic silicide MoSi₂ is a typical radiation agent (Du et al., 2016; Li et al., 2018) with high melting point (2020°C), low density (6.24 g/cm³), and excellent oxidation resistance (Shao et al., 2017b). MoSi₂ forms a dense SiO₂ layer during high-temperature oxidation, which prevents oxygen from permeating into the substrate (Liu et al., 2020; Xiao et al., 2020). Wang et al. (2019a) prepared an MoSi₂-based oxidation protective coating on carbon/carbon composites by combining pack cementation and supersonic atmospheric plasma spraying techniques. The weight loss of MoSi₂-based coating at 900°C for 15 h, 1,200°C for 25 h, and 1,500°C for 50 h was 20.57, 4.24, and 2.61%, respectively. Borosilicate glass (BSG) is an excellent binder agent with an amorphous structure. Its low thermal expansion coefficient can effectively adapt to the substrate, which also shows appropriate fluidity and viscosity under high-temperature melting conditions to heal the holes and cracks due to thermal stress (Guan et al., 2020). Wu et al. (2020) prepared scale-like MoSi₂–borosilicate coatings with MoSi₂ as the emittance agent, flake-fused quartz as coarse fillers, and silica sol as a dispersive medium of coating slurry on rigid mullite fibrous ceramics. The scale-like coatings with the crack network went through 25 thermal cycles between 1,500°C and room temperature without peeling and spalling because of the bonding effect of borosilicate glass.

In this work, C/SiO₂ aerogel is selected as the thermal insulation matrix material, and the fiber is used to improve the mechanical properties of the substrate. The fiber-reinforced C/SiO₂ aerogel composition was prepared by precursor conversion, supercritical drying, and subsequent high-temperature treatment. The borosilicate glass selected as a binder agent was prepared by high-temperature melting combined with water quenching. A gradient coating was designed to alleviate the thermal stress defects caused by thermal expansion mismatch, which was prepared using slurry brushing and rapid sintering methods. The microstructure, radiative property, and static oxidation resistance were investigated in detail.

Experimental

Preparation of Fiber-Reinforced C/SiO₂ Aerogel Composite

The C/SiO₂ gel was synthesized by using catechol (C), formaldehyde (F), and 3-aminopropyltriethoxysilane (APTES) as precursors and ethanol (EtOH) as the solvent. Catechol and formaldehyde are used as the carbon sources, and APTES not only functions as a silica source but also plays a part as a gelation agent. Firstly, a mixture is prepared with a molar ratio of C: F: EtOH = 1:2:15, stirring for about 60 min at room temperature. Subsequently, the desired amounts of APTES (molar ratio of APTES: C = 0.75:1) were dropped into a clear solution. After stirring for 10 min at room temperature, the carbon fiber felt was impregnated with the sol prepared above. After gelation, aging, and solvent exchange, the fiber felt/wet gel was dried under supercritical CO₂ conditions (315 K, 10 MPa) to produce the fiber-reinforced CF/SiO₂ precursor aerogel composite. The precursor aerogel composite was put into the furnace at a rate of 3 K/min to 1073 K under the protection of the argon atmosphere for 150 min. After cooling to room temperature, the composite was heat-treated again at a rate of 3 K/min to 1473 K in a flow of high-purity argon for 180 min.

Preparation of MoSi₂–Borosilicate Glass Coating

Fiber-reinforced C/SiO₂ aerogel composites (ρ = 0.31 g/cm³) were used as the substrates. The borosilicate glass was prepared by high-temperature melting and subsequent water quenching methods, which has been reported in our previous work (Shao et al., 2015). The raw materials including MoSi₂, borosilicate glass powder, and SiB₆ were weighed in the mass ratio 5:44:1. The raw materials, ethanol, and carboxymethylcellulose (CMC) aqueous solution (1 wt%) were mixed in nylon containers and ball-milled by a planetary mill at a rotation speed of 280 rpm for 2 h. The mass ratio of the powders, ethanol, and CMC aqueous solution in the outer coating and inner coating was 6.11:4:1 and 3.33:4:1, respectively. The obtained slurry was uniformly coated on the surface of fiber-reinforced C/SiO₂ aerogel by wool brush and dried in a drying oven at 373 K for 12 h. Then, the as-coated samples were embedded in graphite powder and put into the furnace at 1473 K for 30 min in air. Three coatings were obtained by changing the contents of MoSi₂ in the outer layer (30, 40, and 50%), namely, M30, M40, and M50, respectively.

Static Oxidation Test

Static oxidation tests were carried out in the air in an electrical furnace in order to obtain isothermal oxidation behavior of the multilayer MoSi₂–borosilicate glass–coated fiber-reinforced C/SiO₂ aerogel at 1473 K. The samples were directly placed inside a furnace at 1473 K for a certain time. Subsequently, they were taken out and cooled at room temperature. After weighing the samples’ mass, they were put into the furnace again for oxidation tests. The mass loss ∆m% was calculated using the following equation:

$▵m\%=\frac{m_0-m_1}{m_0}\times 100\%,(1)$

where $m_0$ is the original mass of the coated aerogel composites and $m_0$ is the mass of the coated aerogel composites after oxidation at high temperature.

Radiation Property Test

The room temperature spectral reflectance of the coatings was measured by using a UV-Vis-NIR spectrophotometer in the wavelength range of 0.3–2.5 μm, with BaSO₄ as the reflectance sample. The total emissivity can be calculated according to the following equations:

${\epsilon }_T=\frac{{{\displaystyle \int }}_{{\lambda }_1}^{{\lambda }_2}[1-R\left(\lambda \right)]P_B\left(\lambda \right)d\lambda }{{{\displaystyle \int }}_{{\lambda }_1}^{{\lambda }_2}{P}_B\left(\lambda \right)d\lambda },(2)$

$P_B\left(\lambda \right)=\frac{C_1}{{\lambda }^5[\exp \left(\frac{C_2}{\lambda T}\right)-1]},(3)$

where λ is the wavelength, R(λ) is the reflectance, P_B(λ) is given by Planck’s law, C₁ = 3.743 × 10⁻¹⁶ Wm², and C₂ = 1.4387 × 10⁻² mK.

Characterization of the Coatings

The phase composition of glass and the coating surface were examined using a Rigaku Miniflex X-ray diffractometer (XRD) with Cu-Kα radiation (λ= 0.15406 nm). The microstructure of the composites was surveyed using a scanning electron microscope (SEM, Hitachi S-4800, Japan). X-ray photoelectron spectroscopy (XPS) measurements were performed on a Thermo K-Alpha spectrometer (Thermo Fisher Scientific, Inc., MA). Thermal gravimetric analysis (TGA) was carried out with a thermogravimetric analyzer (STA449F3, Netsch, Germany) under constant nitrogen flow at a heating rate of 10°C/min to 1,400°C. A Nexus 670 Fourier infrared spectrometer (FT-IR spectrometer, Thermo Nicolet Corporation, United States) was employed to analyze the chemical bonds in the aerogel composite and borosilicate glass.

Results and Discussion

Characterization of the Fiber-Reinforced C/SiO₂ Composite Aerogel

The fiber-reinforced C/SiO₂ aerogel composite exhibits low density (0.31 g/cm³) and low thermal conductivity (0.044 W/m*k), which is suitable for high-efficiency thermal insulation uses. The XRD patterns and FT-IR spectrum are shown in Figure 1. The XRD spectrum contains a broad bump at 22° after heat treatment. This is because the organic groups in the precursor aerogel are decomposed to generate H₂O, CO₂, and other gases in high-temperature environments, which makes the composite present an amorphous structure. In particular, peaks at 36°, 43°, 63°, and 76° assign to the aluminum phase, which attributes to the fact that the sample tray is made of aluminum. As we can see in the FT-IR spectrum, the absorption peaks at the wavenumber of 3,438 cm⁻¹ and 1,637 cm⁻¹ come from the water molecules adsorbed inside the aerogel structure. The vibration at 1,100 cm⁻¹ belongs to the Si-O-Si asymmetrical stretching vibration peak, and the vibration at 469 cm⁻¹ assigns to the Si-O-Si bending vibration peak. Moreover, the appearance of the Si-C absorption peak at the wavenumber of 830 cm⁻¹ shows that the aerogel structure changes from organic to inorganic after heat treatment.

FIGURE 1

FIGURE 1. (A) XRD patterns of the fiber-reinforced C/SiO₂ aerogel composite before and after heat treatment. (B) FT-IR spectrum of the fiber-reinforced C/SiO₂ aerogel composite.

Figure 2 presents that the particle and the pore structure distribution of C/SiO₂ aerogel are relatively uniform with a three-dimensional network structure after heat treatment. Aerogel particles are attached to the surface of carbon fibers through physical adsorption. The pore size distribution of the fiber-reinforced C/SiO₂ aerogel composite is shown in Figure 3. The average pore size of the composite is 18.46 nm and mainly distributed between 15 and 25 nm. The Brunauer–Emmett–Teller (BET) test has limitations, so the result of the mercury intrusion method is shown in Figure 3B. The composite presents a macro-porous structure, and its pore size is distributed between 10 and 30 μm, which corresponds to the characteristic of the fiber. The TG curve of the fiber-reinforced C/SiO₂ aerogel composite in the argon environment from room temperature to 1,200°C is presented in Figure 4. The composite has excellent thermal stability with a weight loss of 1.89% at 1,200°C, which is suitable for use as a high-efficiency insulation material.

FIGURE 2

FIGURE 2. SEM image of the fiber-reinforced C/SiO₂ aerogel composite.

FIGURE 3

FIGURE 3. Pore size distributions of the fiber-reinforced C/SiO₂ aerogel composite using the (A) BJH method and (B) mercury intrusion method.

FIGURE 4

FIGURE 4. TG curve of the carbon fiber–reinforced C/SiO₂ aerogel composite.

Characterization of the Prepared Coatings

The component proportion of three coatings is shown in Table 1. To analyze the phase of the coating surface, XRD patterns are presented in Figure 5. A broad peak appears near 22° due to the presence of the glass phase with an amorphous structure. With the increase of MoSi₂ content in the original component, the intensity of the MoSi₂ diffraction peak in the spectrum also increases synchronously. In addition to the oxidation of MoSi₂, the formation of the SiO₂ phase also resulted from the cooling of the borosilicate glass component. Mo₅Si₃, Mo, MoO₂, and MoO₃ phases are identified in the coating because of the oxidation of the radiation agent MoSi₂. The relevant chemical reaction formula is as follows:

$5MoS{i}_2\left(s\right)+7O_2\left(g\right)=M{o}_{5}S{i}_3\left(s\right)+7Si{O}_2\left(s\right),(4)$

$MoS{i}_2\left(s\right)+2O_2\left(g\right)=Mo\left(s\right)+2Si{O}_2\left(s\right),(5)$

$MoS{i}_2\left(s\right)+3O_2\left(g\right)=Mo{O}_2\left(s\right)+2Si{O}_2\left(s\right),(6)$

$2MoS{i}_2\left(s\right)+7O_2\left(g\right)=2Mo{O}_3\left(g\right)+4Si{O}_2\left(s\right).(7)$

TABLE 1

TABLE 1. Compositions of the coatings.

FIGURE 5

FIGURE 5. XRD patterns of the coatings with different contents of MoSi₂.

Figure 6 displays the surface SEM images of coatings with different contents of MoSi₂. The M30 coating surface presents a rough morphology, while the M50 coating exhibits visibly spreading cracks. In addition to the mismatch of thermal expansion coefficients (Wang et al., 2019b), the formation of cracks is also due to the volume effect of the SiO₂ crystal transformation. Comparing the SEM images of M30 and M50 coatings, the surface of the M40 coating is relatively flat and dense and has no obvious thermal stress defects. The M40 coating contains appropriate content of borosilicate glass, which provides suitable fluidity during the preparation process and effectively alleviates thermal stress defects.

FIGURE 6

FIGURE 6. Surface SEM images of the coatings with different contents of MoSi₂: (A) M30; (B) M40; (C) M50.

Figure 7 presents that coatings show a gradient structure. From the further analysis of the EDX spectrum, the content of MoSi₂ presents a decreasing trend from top to bottom, which relieves the mismatch of thermal expansion coefficients between the coatings and the substrate. The M40 coating has a thickness of 350 μm, mainly consisting of two parts: the surface coating layer (zone Ⅰ) of 190 μm and the interfacial transition layer (zone Ⅱ) of 160 μm. It can be clearly observed that the M40 coating has an excellent combination with the substrate and no obvious cracks are discovered. Compared with the M40 coating, cracks with different sizes form on the section of M30- and M50-coated samples, which may result in the failure of the sample during use.

FIGURE 7

FIGURE 7. Sectional SEM images of the coatings with different contents of MoSi₂: (A) M30; (B) M40; (C) M50; (D–F) EDX analyses of the coatings.

Radiation Property of the Coatings

Figure 8 reveals the emissivity curves of coatings with different contents of MoSi₂. The emissivity values gradually increase in the wavelength range of 300–800 nm and reduce in the wavelength range of 801–2,500 nm. The M30 and M40 coatings exhibit higher emissivity than the M50 coating and exceed 0.80 in the wavelength range of 350–2,500 nm. Table 2 shows the calculated total emissivity values in all kinds of wavelength ranges. According to Wien’s displacement law, λ_max = b/T, with b = 2.898 × 10⁻³ m K; as temperature increases, the maximum spectral emissive power shifts to smaller wavelengths. Therefore, when the temperature is in the range of 1,473–2273 K, the largest radiation wavelength corresponds to the range of 1,270–1967 nm. In this range of wavelengths, the MoSi₂–borosilicate glass coatings exhibit a higher emissivity than 0.8, and the total emissivity of M30 and M40 coatings exceeds 0.85.

FIGURE 8

FIGURE 8. Emissivity and absorptivity of the coatings with different contents of MoSi₂.

TABLE 2

TABLE 2. Calculated total emissivity values in various ranges of wavelengths.

Oxidation Resistance of the Coatings

It can be seen from Figure 9A that fiber-reinforced C/SiO₂ aerogel without coating basically oxidized and failed at 60 min, while other coated samples present great oxidation resistance. Especially, the M40 coating has the mass loss of only 0.27%. The M40 coating has suitable viscosity because of the appropriate component of binder, which can bridge defects and block oxygen diffusion channels. However, only the static oxidation test is incapable of deciding the strength of oxidation resistance. The morphology of coating after oxidation and interface between the coating and the substrate still needs further investigation.

FIGURE 9

FIGURE 9. Isothermal oxidation at 1,200°C for 180 min in air. (A) Mass loss curves of the coatings. (B) XRD patterns of the coatings with different contents of MoSi₂.

The XRD pattern of coatings after isothermal static oxidation at 1,200°C for 180 min is demonstrated in Figure 9B. Compared with the original components of coatings before oxidation, the diffraction peak of MoSi₂ is significantly reduced, while the diffraction of crystalline SiO₂ is enhanced. The oxidation of MoSi₂ forms volatile MoO₃ and crystalline SiO₂. Comparing the phase composition of the coatings with different MoSi₂ contents after oxidation, the amorphous nature of glass near 22° can be observed in all samples, indicating the coating surfaces include the borosilicate glass. Especially, the surface of M40 and M50 coatings has more content of borosilicate glass. Moreover, Mo, MoO₂, Mo₅Si₃, and MoO₃ are supposed to form under different partial pressure of oxygen.

As shown in Figure 10A, O1s, Mo3d, B1s, Si2s, and Si2p peaks exist on the surface of coating before oxidation. After isothermal oxidation for 180 min, the intensity of the O1s and Mo3d peaks increased significantly. It is well known that XPS is a useful tool for directly measuring relatively bridging oxygen (BO) and non-bridging oxygen (NBO) concentrations (Sossaman and Perepezko, 2015). It can be seen from Figure 10B that a BO atom contains two bands with energies at 533.00 eV, while NBO atoms possess a single bond and a partial negative charge with the binding energy at 531.20 eV. Similarly, Figure 10C displays the O1s spectrum can be described by two components with binding energies at 532.60 eV (BO) and 530.40 eV (NBO) after oxidation. By calculating the peak area, the NBO concentration of the oxidized layer (19.84%) is reduced by 4.67% compared to that of the original layer (24.51%). It presents crystallization of SiO₂, volatilization of B₂O₃, and an increase in viscosity during the oxidation test, which corresponds to the result of XRD. Figures 10D,E present high-resolution core-level XPS spectra of the Mo3d peak of the as-prepared coating and the coating after oxidation at 1,200°C for 180 min. The binding energies of Mo3d_3/2 and Mo3d_5/2 for the as-prepared coating are 235.98 and 28.1 eV, respectively. After oxidation at 1,200°C for 180 min, the coating presented Mo3d_3/2 and Mo3d_5/2 values of 235.36 and 232.35 eV, respectively, which are a characteristic of MoO₃ (Sun et al., 2020). In particular, the peaks of Mo3d_3/2 at 231.00 eV before oxidation and 230.45 eV after oxidation and the peaks of Mo3d_5/2 at 228.60 eV before oxidation and 228.86 eV after oxidation are all derived from Mo, which has a good match with the XRD result. However, the diffraction peak of MoO₂ shown in the XRD was not detected in XPS. It may be because the XRD penetration depth is within tens of micrometers related to the tested materials, while the photoelectron escape depth of the tested material is only approximately 10 nm. These results indicate that MoO₂ mainly formed at a depth of tens of micrometers, which is consistent with the fact that MoO₂ formed under low oxygen partial pressure.

FIGURE 10

FIGURE 10. XPS pattern of the M40 coating before and after isothermal oxidation. (A) Wide scan XPS spectra; (B) O1s of the prepared coating; (C) O1s of the coating after oxidation at 1,200°C for 180 min; (D) Mo3d of the prepared coating; (E) core-level XPS spectra of Mo3d of the coating after oxidation at 1,200°C for 180 min.

The surface and cross-sectional SEM images of the M40 coating oxidized at 1,200°C for 180 min are shown in Figure 11. Compared to the original coating surface, it can be seen from Figure 11A that the surface of the coating has no obvious pores and cracks after oxidation. It is mainly because the volatile products are blocked and then “covered” by borosilicate glass during high-temperature oxidation, resulting in unevenness morphology. According to EDX analysis (Figure 11D, E, F), the coating surface exhibits a large amount of elements Si and O, which indicates that amorphous glass formed during oxidation plays roles of healing pores and cracks, while the element of Mo is rare on the coating surface, which is basically consistent with the XRD result.

FIGURE 11

FIGURE 11. SEM images of the coatings after isothermal oxidation at 1,200°C for 180 min in air: (A, B) surface; (C) section; (D) EDX analyses; (E, F) EDX mapping analysis.

To explain the oxidation mechanisms of the MoSi₂–borosilicate glass–coated fiber-reinforced aerogel samples during isothermal oxidation, a schematic diagram is displayed in Figure 12. During the oxidation process, the thermal stress due to the mismatch of coefficients of thermal expansion between the coating and the substrate would lead to the cracking of the coating (Chu et al., 2015). However, the borosilicate glass exhibits appropriate fluidity and viscosity at high temperature, which could seal the penetrated cracks in the coating, as presented in Figure 12A. With the increasing time of oxidation, the cracks of coating are getting larger and borosilicate glass consumes gradually. On the one hand, some oxygen diffuses to the MoSi₂–borosilicate glass coating through cracks and then reacts with coating and releases some gases such as SiO and MoO₃ (indicated by black arrows in Figure 12B). On the other hand, some oxygen diffuses to fiber-reinforced aerogel through penetrating cracks, resulting in the oxidation of the substrate and generating CO₂ and CO gases (indicated by red arrows in Figure 12B). These gases would accumulate with the gases produced by the oxidation of coating, forming bubbles on the surface of the coating. At this time, if borosilicate glass still has good fluidity, it would cover the bubbles and form a “bulge” morphology, as shown in Figure 11B, whereas the bubbles would break and form pores due to the pressure of gases exceeding the surface tension of bubbles. And oxygen further diffuses to fiber-reinforced aerogel, resulting in the failure of samples (Li et al., 2020b).

FIGURE 12

FIGURE 12. Schematic diagram of possible oxidation mechanisms of the coated fiber-reinforced aerogel samples during isothermal oxidation. (A) oxidation early period; (B) oxidation later period.

Conclusion

This new thermal protection system is based on fiber-reinforced C/SiO₂ aerogel as the matrix, and the slurry method combined with the embedding sintering method is used to prepare a gradient MoSi₂–borosilicate coating on its surface. The coating has a thickness of 350 μm and exhibits a gradient structure: an outer surface coating of 190 μm and a transition coating of 160 μm inside. It also alleviates the thermal expansion coefficient mismatch of each part, which contributes to the acquisition of excellent high-temperature thermal stability. The M30 coating exhibits excellent radiation property with a total emissivity of 0.8722 in the wavelength range of 1,270∼1967 nm. The MoSi₂–borosilicate coatings were oxidized at a static temperature of 1,200°C for 180 min, showing excellent thermal stability. The M40 coating has remarkable antioxidant property with a weight loss of only 0.27%. This is mainly attributed to the appropriate viscosity and fluidity of the binder, which not only has the function of bridging defects but also has the effect of blocking oxygen diffusion channels. This composite material has broad application prospects in thermal protection.

Data Availability Statement

The raw data supporting the conclusions of this article will be made available by the authors, without undue reservation.

Author Contributions

TD performed the experiment. ZS contributed significantly to manuscript preparation. YD and ZS performed the data analyses. YZ helped perform the analysis with constructive discussions. SC contributed to the conception of the study.

Funding

This work was financially supported by the Key Research and Development Project of Jiangsu Province (BE2019734), the Major Program of Natural Science Fund in Colleges and Universities of Jiangsu Province (15KJA430005), the National Natural Science Foundation of China (51702156, 81471183), the Postgraduate Research and Practice Innovation Program of Jiangsu Province (KYCX19_0837), and the General Program of Natural Science Fund in Colleges and Universities of Jiangsu Province (19KJB430023).

Author Disclaimer

Any opinions, findings, and conclusions or recommendations expressed in this paper are those of the authors and do not necessarily reflect the views of these programs.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

Publisher’s Note

All claims expressed in this article are solely those of the authors and do not necessarily represent those of their affiliated organizations, or those of the publisher, the editors, and the reviewers. Any product that may be evaluated in this article, or claim that may be made by its manufacturer, is not guaranteed or endorsed by the publisher.

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