Microstructure and Corrosion Behavior of Laser Cladding FeCoNiCrBSi Based High-Entropy Alloy Coatings

: High-entropy amorphous alloys designed based on the concept of multi-principal components have the comprehensive advantages of high passivation element content and amorphous structure, and are considered as one of the promising alternative protective materials in extreme marine environments. However, based on the composition of traditional amorphous alloys, the multi-principal design significantly reduces its glass forming ability. In order to improve the glass formation ability of high-entropy amorphous alloys, this study attempts to design Fe 19.6 Co 19.6 Ni 19.6 Cr 19.6 (B 13.72 Si 5.88 ) 19.6 Y 2 alloy by microalloying on the basis of traditional FeCoNiCrBSi high-entropy amorphous alloy. The traditional Fe 43.6 Co 6 Ni 17.4 Cr 9 B 17.5 Si 1.5 Nb 5 iron-based amorphous alloy was selected as the comparison material. Then, spherical alloy powders were prepared by gas atomization. The amorphous nanocrystalline composite coatings were deposited on the 304 stainless steel by laser cladding technology. The microstructure of the coatings was characterized by scanning electron microscopy and X-ray diffractometer. The corrosion behavior of laser cladding coatings in 3.5 wt.% NaCl solution were investigated in detail. The results show that the Fe 43.6 Co 6 Ni 17.4 Cr 9 B 17.5 Si 1.5 Nb 5 powder is composed of FCC, Laves and boride phases. Whereas the Fe 19.6 Co 19.6 Ni 19.6 Cr 19.6 (B 13.72 Si 5.88 ) 19.6 Y 2 high-entropy amorphous alloy powder is composed of FCC and boride phases. Due to the remelting and multiple heat treatments during the preparation of the laser cladding coatings, borides were precipitated in both coatings. The microstructure of the two coatings from the bonding area with the substrate to the top layer are plane grains, dendrite, equiaxed grains and amorphous phase, respectively. Fe 19.6 Co 19.6 Ni 19.6 Cr 19.6 (B 13.72 Si 5.88 ) 19.6 Y 2 high-entropy amorphous alloy coating exhibits high corrosion potential, passivation ﬁlm resistance and low corrosion current density in 3.5 wt.% NaCl solution. In addition, the passivation ﬁlm formed on the coating has higher Cr content and lower defect concentration, showing more excellent corrosion resistance. Author Contributions: Conceptualization, W.G. and B.L.; methodology, H.Z.; software, H.Z., J.Z. and W.L.; validation, B.L., W.G. and Z.D.; formal analysis, Z.D.; investigation, H.Z., W.L., H.X. and L.C.; resources, W.G. and B.L.; data curation, W.L., H.X. and L.C.; writing—original draft preparation, H.Z.; writing—review and B.L. and W.G.; visualization, Z.D.; supervision, B.L.; project administration, and B.L.; funding acquisition, and B.L. authors read agreed


Introduction
Under the combined influence of corrosion, working load and environmental load, large-scale marine engineering equipment usually suffers from harsh service environments [1,2]. Due to the excellent mechanical properties, corrosion resistance and wear resistance, Fe-based amorphous alloy coatings are one of the promising candidates for the design of anti-corrosion and wear-resistant integrated coatings [3]. However, in Fe-based amorphous alloys, the content of passivation elements such as Co, Ni, and Cr is limited, which will weaken its passivation performance in corrosive environments. This is because the atomic radius of elements such as Co, Ni, Cr and Fe are very close, and high content of Co, Ni and Cr will not be conducive to increasing the atomic size difference in the alloy

Preparation of Gas Atomized Powders
High-purity Fe, Co, Ni, Cr, B, Si, and Y elements (99.99%) were selected as raw materials. High-entropy alloy ingots with uniform composition was obtained by multiple arc melting according to the chemical composition shown in Table 1. The alloy ingots were cut into the raw material size required for gas atomization powder preparation process by mechanical processing. Then, spherical powders were prepared by induction melting and argon atomization (HERMIGA 100-30 V2ICC, Peshing New Metal Material Co., Ltd., Changzhou, China). The prepared powder was processed by air classification. FeCoNiCrBSiY (45-106 µm) and Fe 43.6 Co 6 Ni 17.4 Cr 9 B 17.5 Si 1.5 Nb 5 powders (53-106 µm) were selected as raw materials for the preparation of laser cladding coatings. Figure 1 presents the particle size distribution of the powders.

Preparation of Laser Cladding Coatings
SUS304 stainless steel is selected as the base material, and its chemical composition is shown in Table 2. The stainless steel was cut into samples with dimensions of 100 mm × 100 mm × 6 mm. Before preparing the coating, the surface of the sample was ground with sandpaper, cleaned with alcohol, and then dried. The coatings were deposited on a 100 mm × 100 mm surface of the stainless steel substrate using a JM-RB-3000 laser cladding system (Wuhan Precision Laser Technology Co., Ltd., Wuhan, China) with coaxial powder feeding. High-purity argon was used as the protective gas in the coating preparation process. The laser cladding process parameters of the two coatings are shown in Table 3. The overlap ratio of adjacent cladding layers is selected as 35 %, and the coating is obtained by single-layer multi-pass cladding.

Microstructural Characterization of Powders and Coatings
An AL-2700B X-ray diffractometer was used to analyze the phase structures of the powders and coatings (Dandong Aolong Radiative Instrument Group Co., Ltd., Dandong, China). The target material was Cu target, and the working voltage and current were 40 kV and 30 mA, respectively. The scanning range (2θ) was 10~90 • , and the scanning speed was 5 min/•.
After mixing the prepared alloy powder with phenolic resin, metallographic samples for microstructure characterization of the powders were prepared using an XQ-1 metallographic sample inlay machine (Shanghai Caikon Optical Instrument Co., Ltd., Shanghai, China). The samples were ground with sandpaper and polished to a mirror surface with 0.3 µm diamond paste. The FeCoNiCrBSiNb and FeCoNiCrBSiY coatings were cut into 10 mm × 10 mm × 8 mm samples. The cross-section of the two coatings was also ground with sandpapers and then polished. The cross-sectional morphology and chemical composition of the powders and coatings were characterized by Oxford scanning electron microscopy with energy dispersive spectroscopy (Oxford Instruments Technology Ltd., Oxford, UK).

Corrosion Behavior of Laser Cladding Coatings
An electrochemical station (Multi Autolab M204, Hongkong, China) with a threeelectrode cell system was used to measure the potentiodynamic polarization (PDP) and electrochemical impedance spectroscopy curves (EIS) of the coatings. Before testing, the stainless steel substrate of the coated samples was welded with Cu wire. Then, the samples were cold mounted with resin. Only the coated surface was exposed as a working surface with an area of 1 cm 2 . To ensure the same surface roughness for all coated samples, all coatings were ground and polished. The corrosion behavior of the coatings was investigated in 3.5 wt.% NaCl solution at room temperature. A platinum sheet and a saturated calomel electrode (SCE) were used as counter electrode and reference, respectively.
Before corrosion performance characterization, all prepared samples were soaked in 3.5 wt.% NaCl solution for 30 min to reach a stable open circuit potential (OCP). Then, the EIS measurements were performed in a frequency range from 100 kHz down to 10 mHz at OCP using a 10 mV signal amplitude. The PDP tests were started from −0.5V and ends at 1.5 V versus OCP at a potential scan rate of 1 mV/s. The impedance data was interpreted by using the Zsimpwin software and equivalent electron circuits.

Characterization of the Passivation Film
The coating samples was held potentiostatically at 1 V for 1 h in the 3.5 wt.% NaCl solution to form a stable passivation film. Then, X-ray photoelectron spectroscopy (XPS) was used to analyze the composition of the passivation film. The commercial software XPSpeak (version 4.1) was used to analyze XPS data. The semiconducting properties of the passivation films were analyzed by Mott-Schottky (M-S) plots. The M-S plots were performed within the potential range from −1.0 V SCE to 0.5 V SCE . The scanning rate was 50 mV/steps at a perturbation voltage of 10 mV and a fixed frequency of 1 kHz. Figure 2 shows the microstructure of the FeCoNiCrBSiNb and FeCoNiCrBSiY powders. The powder particles of both alloys exhibited good spherical shape with smooth surfaces.

Microstructure of the Gas Atomized Powders
There are a few pores on the surface of the powder particles. FeCoNiCrBSiNb powder contains a small amount of circular precipitates, the average content of which is about 11% measured by grayscale method. There are a large number of strip-like precipitates in FeCoNiCrBSiY powder, with an average content of about 75%. Table 4 shows the EDS analysis results in Figure 2b,d. It can be seen from Table 4 that the content of B element in the precipitation phase of the two powders is relatively high, indicating that borides are formed inside the powders.    Figure 3 illustrates the X-ray diffraction (XRD) patterns of the powder and laser cladding coatings. The results show that FeCoNiCrBSiNb powder is composed of facecentered cubic solid solution (FCC), Laves and Cr 2 B. According to the research results in Figure 2 and Table 4, it can be inferred that the precipitates in the powder are solid solution (FCC), Laves and Cr 2 B. In addition, the XRD pattern of the powder showed scattering peaks at 2θ = 51 • and 75 • , indicating that a small amount of amorphous phase or nanocrystals existed in the powder. After the laser cladding process, the FeCoNiCrBSiNb coating consists of face-centered cubic solid solution (FCC), Laves, Cr 2 B, Fe 2 B, Fe 3 B, CoB and Ni 4 B 3 phases. This result is similar to the phase results reported by Guilherme et al. [17] in Fe 63.5 Cr 25 Ni 7 B 4.5 alloy. The diffraction peak of the coating is significantly broadened at 2θ = 51 • , indicating that the coating contains a high content of amorphous or nanocrystalline phases. This is because the powder is remelted and solidified rapidly during the laser cladding process, and the cooling rate of the coating is relatively large. FeCoNiCrBSiY powder is composed of face-centered cubic solid solution (FCC) and Cr 2 B. According to the research results in Figure 2 and Table 4, it can be inferred that the precipitates in the powder are face-centered cubic solid solution (FCC) and Cr 2 B. After the laser cladding process, the FeCoNiCrBSiY coating can be found to be composed of face-centered cubic solid solution (FCC), Cr 2 B, Fe 2 B, Fe 3 B, CoB and Ni 4 B 3 phases. This phenomenon is similar to the findings of Cheng et al. [11] in Fe 25 Co 25 Ni 25 (B 0.7 Si 0.3 ) 25 highentropy alloy coating. The diffraction peaks of the coating at 2θ = 43 • , 51 • and 75 • were significantly broadened, indicating that the content of amorphous phase or nanocrystal in the coating was significantly higher than that of the powder.  Figure 4a that the boundaries between the multiple cladding layers in the FeCoNiCrBSiNb coating are clear. In addition, the white precipitates are mainly distributed in the bottom and middle layers of the coating. However, the difference is that no obvious boundaries between multiple cladding layers are found from the cross-sectional morphologies of the FeCoNiCrBSiY coating ( Figure 4b). The white precipitates are mainly distributed in the bottom layer of the coating. Figure 4c,e,g show the local micro-morphologies of different regions of FeCoNiCrB-SiNb coating. The results show that a large number of dendrites are precipitated in the bottom and middle layers of FeCoNiCrBSiNb coating. This is due to the fact that the liquid metal in the molten pool is in close contact with the matrix grains and completely wets them, so crystals can easily nucleate from the liquid metal on the matrix grains [18]. The solidification rate (V) is slower and the temperature gradient (G) is higher near the bonding area between the coating and the SUS304 substrate, and the larger G/V ratio leads to the formation of larger size dendrites at the bottom of the molten pool [19]. Similar findings were also reported by Cheng et al. [19] and Xiao et al. [20]. Figure 4g indicates that the precipitates in the top layer of the coating are significantly reduced and smaller in size, which is caused by the rapid cooling. The EDS surface scanning analysis results of the middle region of FeCoNiCrBSiNb coating are shown in Figure 5. It can be seen from the figure that the distribution of Fe and Co elements in the middle area of FeCoNiCrBSiNb coating is relatively uniform, while Nb and Cr elements are segregated. The white fine precipitates are rich in Nb elements, and the gray striped precipitates are rich in Cr and Nb elements. According to the XRD pattern analysis results of FeCoNiCrBSiNb coating, it can be inferred that the Nb-rich precipitation phase is Laves and the Cr-rich precipitation phase is Cr 2 B.    (Figure 4h). Figure 6 shows the EDS analysis results of the middle region of the FeCoNiCrBSiY coating. It can be seen from Figure 6 that the strip-shaped precipitates are rich in Cr and depleted in Co and Ni elements. According to the XRD analysis results in Figure 3, the strip-like precipitates in this coating can be inferred to be Cr 2 B.   Figure 7 shows the PDP curves of laser cladding FeCoNiCrBSiNb and FeCoNiCrBSiY coatings. Table 5 lists a series of electrochemical parameters fitted from PDP curves. E corr and i corr represent corrosion potential and corrosion current, respectively. The β a and β c are the slopes of the anodic and cathodic Tafel polarization curves, respectively. The polarization resistance (R p ) of the coating is calculated according to the Stern-Geary Equation (1) [21].

PDP Curves
In general, high corrosion potential and low corrosion current density indicate materials with higher chemical stability and lower corrosion tendency [22]. Compared with the FeCoNiCrBSiNb coating, the FeCoNiCrBSiY coating exhibits high corrosion potential, low corrosion current density, and large polarization resistance, indicating better corrosion resistance.   [25] −458 1.13 × 10 −5 --- Table 5 lists the electrochemical parameters of some high-entropy amorphous alloys and Fe-based amorphous alloy coatings reported in the literature under the same experimental conditions. Literature studies have shown that the corrosion resistance of amorphous coatings is closely related to the compactness, passivation elements and amorphous phase content of the coating. The amorphous phase content of the magnetron sputtering Ti 21.6 Al 11.3 Cr 19.4 Si 23.5 V 22.0 O 2.2 high-entropy amorphous coating reported by Lin et al. [23], the atmospheric plasma sprayed Fe 87.6 Cr 2.5 Si 6.7 B 2.5 C 0.7 coating reported by Bijalwan et al. [24], and the HVOF sprayed Fe 48 Cr 15 Mo 14 C 15 B 6 Y 2 coating reported by Huang et al. [25] are as high as 100%, 93.40% and 88.95%, respectively. However, due to the high porosity or low content of passivating elements in the above coatings, their corrosion resistance is limited [26,27]. The research results of Berger et al. [28] showed that a stable passivation film can be formed on the alloy surface only when the chromium content is higher than 17%. It has been reported in the literature that the effect of the content of passivating elements in amorphous alloys on its corrosion resistance may be more important than the effect of the amorphous structure itself [29,30]. Botta et al. [31] confirmed the key role of Cr on the corrosion performance of Fe-based amorphous alloys, and Fe-based amorphous alloys without passivation elements had poor corrosion resistance.
The laser cladding high-entropy amorphous-nanocrystalline composite coatings reported in this study are highly dense. In addition, high-purity argon is used as a protective gas during the coating cladding process, which prevents the molten pool from being oxidized. There are almost no pores and oxides in the laser cladding coating, which significantly reduces the diffusion path of corrosion ions. The high content of passivation elements such as Co, Ni and Cr in the FeCoNiCrBSiY high-entropy amorphous alloy coating improves the corrosion resistance of the coating.

Electrochemical Impedance Spectroscopy
The EIS measurement results of laser cladding FeCoNiCrBSiNb and FeCoNiCrBSiY coatings are illustrated in Figure 8. The Nyquist plots of both coatings in 3.5 wt.% NaCl solution (Figure 8b) are incomplete semi-circles, indicating that the corrosion process of the coatings is controlled by the charge transfer process. Generally speaking, a large capacitive arc radius indicates high corrosion resistance [32]. It can be seen from Figure 8b that the capacitive arc radius of FeCoNiCrBSiY coating is significantly larger, which indicates that FeCoNiCrBSiY coating has stronger resistance to electrochemical corrosion and forms a more protective passivation film on its surface. The Bode plot (Figure 8c) shows that the slope (−0.9) of the logZ-logf curves of the two coatings is close to −1, which means that the passivation film formed on the coatings has capacitance-like properties. Furthermore, the Phase-logf plots of both coatings (Figure 8d) have only one peak, which means there is only one time constant. According to the equivalent circuit of R s (Q film R film ) proposed in [33], the EIS data of this study were fitted with Zsimpwin software. R s represents the resistance of the solution. A passivation film and an electric double layer exist at the electrode/electrolyte solution interface, and R film is the total resistance of the passivation film and the electric double layer. Studies have shown that the passivation film has a high charge transfer resistance, and the charge transfer resistance value mainly depends on the passivation film [34]. The lower the R film value, the easier it is for the charge to pass through the passivation film [35]. Equivalent capacitance Q film (constant phase angle element CPE) is used for fitting instead of pure capacitance C [36]. The equivalent circuit diagram is shown in Figure 6a, and the fitting parameters are shown in Table 6. The Chi-squared (χ 2 ) values is related to the fitting accuracy [34]. The order of magnitude of χ 2 values for both coatings is 10 −4 , indicating that it is reasonable to use the R s (Q film R film ) equivalent circuit to fit the EIS data in this study.  It is reported in the literature that the capacitance of the passivation film on the coating can be represented by the equivalent capacitance Q [37]. Q includes the constant Y 0 (Ω −1 ·cm −2 ·s −n ) and dimensionless exponent n. n is the deviation value from pure capacitive behavior. The closer the system is to an ideal capacitance, the closer the value of n is to 1 [38]. It can be found from Table 6 that the Q film -Y 0 value (6.9 × 10 −4 Ω −1 ·cm −2 ·s −n ) of FeCoNiCrBSiY coating is smaller, indicating that the passivation film formed on its surface is thicker and denser [39,40]. The higher R film value of FeCoNiCrBSiY coating indicates that its surface passivation film is stable and less sensitive to anions in solution. Figures 9 and 10 show the X-ray photoelectron spectroscopy (XPS) of the passivation films formed by FeCoNiCrBSiNb and FeCoNiCrBSiY coatings in 3.5 wt.% NaCl solution, respectively. Figures 8a and 9a show the spectra of Fe, Co, Cr, Ni and O, while the C peak is associated with inevitable air pollution. There is a main O peak in the measured energy spectra of FeCoNiCrBSiNb and FeCoNiCrBSiY coatings, which confirms the formation of oxide films on the coating surfaces.   3 , respectively [33]. Figures 9c and 10c show the Co 2p3/2 spectra of the two coatings, the peak at 780.7 eV corresponds to Co 3+ and the peak at 785 eV corresponds to Co sat (an unanalyzed companion peak) [41,42]. Figures 9d and 10d show the binding energy components of the Fe 2p3/2 spectrum at 710 eV and 711.8 eV on the passivation films for the two coatings, representing Fe ox 3+ and Fe hy 3+ , respectively. This is similar to the results reported in CoCrFeMnNi high-entropy alloys [39]. The deconvolution results of iron species show that the main component in the passivation films of the two coatings is iron hydroxide. Figures 9e and 10e show the Ni 2p3/2 spectra of the passivation films of the two coatings, the peak at 855.7 eV corresponds to Ni(OH) 2 and the peak at 859.2 eV corresponds to Ni sat (Unanalyzed companion peak) [43]. The O1s spectra obtained from the passivation films on FeCoNiCrBSiNb and FeCoNiCrBSiY coatings are divided into 2 components (Figures 9f and 10f). O 2− species (530.2 eV) mainly exist in the form of Cr and Fe oxides. The peak at 531.8 eV represents OH − species, which exist in the passive film as metal hydroxides. Figure 11 shows the atomic percentages of Fe, Co, Cr and Ni in the passivation films of FeCoNiCrBSiNb and FeCoNiCrBSiY coatings. It is obviously found that the passive film on the surface of FeCoNiCrBSiY coating contains lower Fe content and higher Cr content. The Cr/Fe ratios in the passivation films which formed on the FeCoNiCrBSiNb and FeCoNiCrBSiY coating are 0.15 and 1.8, respectively. This means that the passivation film on the surface of FeCoNiCrBSiY coating contains high content of Cr oxide or hydroxide, which is beneficial to improve its compactness and stability.

Mott-Schottky Curves
In general, passivation films on metal surfaces exhibit semiconducting behavior [44]. By adjusting the applied voltage, the majority carriers in the oxide space charge layer can be taken out to make the layer in a depleted state. Figure 12 shows the Mott-Schottky plots of the passivation films on the surfaces of FeCoNiCrBSiNb and FeCoNiCrBSiY coatings. According to the mott-schottky theory, the capacitance of the p-type semiconductor space charge layer can be calculated according to formula (2) [45].
where N A is the doping density; ε r is the dielectric constant of the passive film, which usually takes a value of 12 [46]; ε 0 is the permittivity of the vacuum (8.854 × 10 −14 F·m −1 ); k is the Boltzmann's constant; e is the electron charge; E FB is the flat band potential; T is the absolute temperature; and kT/e is negligible (about 25 mV at room temperature). It can be seen from Figure 12a that the Mott-Schottky curves of FeCoNiCrBSiNb and FeCoNiCrBSiY coatings exhibit linear forms in the range of 0.33 V SCE~0 .80 V SCE and 0.21 V SCE~0 .80 V SCE , respectively. The Mott-Schottky linear relationship with negative slope indicates that the passivation films formed by both coatings in 3.5 wt.% NaCl solution have p-type semiconductor properties. The main carriers of p-type semiconductors are cation vacancies [47]. Similar phenomena have been reported in other studies on the properties of metal-semiconductors [48][49][50]. The carrier concentration (acceptor concentration, N A ) and flat band potential (E FB ) can be calculated according to the linear equation fitted in Figure 12a. Figure 12b shows the flat band potential values and acceptor concentration values of the passivation films of the two coatings. The acceptor concentration (N A = 8.3 × 10 24 cm −3 ) of the passivation film of FeCoNiCrBSiY coating is lower than that of FeCoNiCrBSiNb coating (N A = 2.1 × 10 25 cm −3 ), indicating that the passivation film of FeCoNiCrBSiY coating has fewer defects. In addition, the flat band potential (1.04 V) of the passivation film of FeCoNiCrBSiY coating is higher than that of FeCoNiCrBSiNb coating (0.98 V), indicating that the space charge layer of the passivation film on the surface of FeCoNiCrBSiY coating has a more stable structure and is not easily broken down.

Phase Structure of the Coating
It can be seen from Figure 3 that both coatings have crystal phases formed during the laser cladding process. Studies have shown that crystallization is difficult to avoid in laser cladding because the cooling rate in the heat-affected zone is lower than the critical cooling rate required to avoid crystallization [51,52]. The results show that the phases formed by the two coatings are mainly borides, such as Cr 2 B, Fe 2 B, Fe 3 B, CoB and Ni 4 B 3 phases. Similar phenomena have been reported in a large number of literatures [53][54][55][56]. This is related to the binding energy of boron and other metal elements [4]. Table 7 lists the mixing enthalpies of some atom pairs. The mixing enthalpy of Cr-B and Fe-B is relatively negative, which means that Cr and Fe can easily combine with B to form compounds. The phase structures of FeCoNiCrBSiNb and FeCoNiCrBSiY coatings are roughly similar. The difference is that the Laves phase exists in the FeCoNiCrBSiNb coating. According to literature reports [11,19], the Laves phase is (Co,Cr)Nb with a hexagonal closepacked structure. According to literature reports, borides and Laves phase can significantly improve the hardness of the coatings, but they are easy to cause galvanic corrosion and lead to a decrease in the corrosion resistance of the coatings [53][54][55][56]. A large number of studies have shown that Cr is a key element to form a passivation film on the surface of the alloy and improve the corrosion resistance of the alloy [35,36,39,57]. The ratio of Cr/Fe can characterize the chromium enrichment rate of the passive film [58]. It can be seen from Figure 11 that the Cr/Fe ratio (1.8) in the FeCoNiCrBSiY coating passivation film is significantly higher. This shows that there is a higher content of Cr in the passivation film of FeCoNiCrBSiY coating, and Cr exists in the form of oxide and hydroxide. Both Zhou et al. [43] and Zheng et al. [59] reported that a higher Cr/Fe ratio is beneficial for enhancing the compactness and stability of passivation films. Wang et al. [33] and Liu et al. [57] reported that both Cr(OH) 3 and Cr 2 O 3 in the passivation film are beneficial to improve the corrosion resistance of coatings.
According to the Pilling-Bedworth theory, the PBR value of Cr 2 O 3 is greater than 1, resulting in compressive stress in the film [58]. The residual compressive stress can improve the stability of the passive film, resulting in improved corrosion resistance of the coating. In addition, Cr(OH) 3 is beneficial to improve the activity of micropores in the passivation film and its repassivation ability, thereby improving its corrosion resistance [60]. The "water" in the hydrated oxide is believed to maintain the amorphous state of the film, thus maintaining the high corrosion resistance of the passivation film [59]. Figure 12 shows that the passivation films of both coatings exhibit p-type semiconductor characteristics. According to the point defect model, chloride ions are transferred from the electrolyte solution to the oxygen vacancies of the passivation layer and reduce their concentration, thereby increasing the number of cation vacancies in the passivation layer and making the passivation film exhibit p-type semiconductor characteristics [61,62]. It can be seen from Figure 12a that in the potential range of 0.4-0.8 V, the capacitance of the passivation film formed on the surface of the FeCoNiCrBSiNb coating in the chloride-containing environment is significantly higher. This indicates that the porosity of the passivation film is increased due to the diffusion of chloride ions in the passivation layer and causing it to dissolve [63]. Studies have shown that chloride ions in the passivation film accelerate the dissolution of the passivation film through the adsorption and permeation of the acceptor (cation vacancies), thereby reducing the compactness and stability of the passivation film [50]. According to the calculation results in Figure 12b, the FeCoNiCrBSiNb coating passivation film contains more cation vacancies. Anion absorption leads to an increase in the number of cation vacancies at the passivation film/solution interface, which will pass through the passivation film and reach the passivation film/coating interface. If the diffusion rate of cation vacancies is high, the cations generated at the coating/passivation film interface cannot accommodate cation vacancies, so that a large number of cation vacancies aggregate, which will easily lead to local thinning of the passivation film or detachment from the coating [44]. Figure 12b also compares the flat band potential (E FB ) of the passivation films of the two coatings. The Fermi level (E F ) is inversely proportional to the flat band potential (E FB ). Therefore, the Fermi level (E F ) can be easily obtained by the value of E FB [64]. It is well known that the corrosion process is accompanied by the transfer of electrons. In general, the transfer of electrons becomes easier with the increase of the E F value and reduces the corrosion resistance of the passivation film [65]. It can also be seen from Figure 12b that the FeCoNiCrBSiY coating passivation film has a higher flat band potential (1.04 V), which indicates that the FeCoNiCrBSiY coating passivation film has better protection performance. Similar findings were also reported by Zhou et al. [43]. In addition, they also reported that a higher flat-band potential would increase the stability of the space charge layer of the passivation film and make the passivation film more difficult to destroy. In the FeCoNiCrBSiNb coating, the size of the dendrites on top of the coating is significantly reduced. A large number of elongated borides precipitated in the Fe-CoNiCrBSiY coating. Due to the faster cooling rate of the top layer of the coating, the content of the borides decreases and the size becomes smaller. (3) FeCoNiCrBSiY coating exhibits high corrosion potential (E corr = −340 mV), low corrosion current density (i corr = 1.2 × 10 −6 A/cm 2 ), large polarization resistance (R p = 20,000 Ohm·cm 2 ) and high passivation film resistance (R film = 1977 Ohm·cm 2 ) in 3.5 wt.% NaCl solution, showing better corrosion resistance. The passivation film formed on the FeCoNiCrBSiY coating contains higher Cr/Fe ratio, indicating that the passivation film has better compactness.