The Study of Graphene Oxide on the Regulations and Controls of the Sol-Gel Film Structure and Its Performance

: A facile strategy to boost anticorrosion potency of graphene oxide/silica hybrid sol-gel coating is developed through fully exploiting the capabilities of graphene oxide (GO). Together with a barrier to corrosives and crack inhibitor, GO was further explored herein as a regulator to regulate the gelation process and provide robust coating ﬁlms with stratiﬁed microstructures and ultimately extended diffusion paths. The sol-gel coating with stratiﬁed microstructure achieved on AA5052 aluminum alloy surface afforded greatly enhanced corrosion protection capability as assessed by electrochemical measurements and immersion tests. The corrosion current density of the sample of a hybrid GO sol-gel ﬁlm was about 30 times less than that of sample of pure sol-gel ﬁlm sample. The regulation mechanism of GO during the ﬁlm formation process and the anticorrosive protection properties of the ﬁlm were discussed.


Introduction
Aluminum alloys have the advantages of good installation and transportation [1,2], light weight and high specific strength. They are widely used in aerospace, electrical transmission and transformation architecture [3]. By the complex application environment, the application of aluminum alloy is limited [4].
The organic coating, traditionally used, ages after long service, poor UV resistance and emission of toxic VOC, making it unsuitable for application to outdoor environments. Inorganic coating has good wear resistance, UV resistance and environmental friendliness, which can protect aluminum metal components in power transmission and transformation systems in service [5].
Nowadays, inorganic sol-gel coating is becoming an attractive research field for its environmentally friendly features and low cost [6][7][8]. Eco-friendly sol-gel coating is second to none as a prospective candidate to substitute traditional conversion coatings [9]. However, large-scale applications of those inorganic coatings are limited by their brittle nature. It is difficult to fabricate crack-free, thick enough sol-gel coating films with sufficient corrosion protection capabilities [10]. Much effort has been devoted to improving their anti-corrosion performance through the introduction of functional additives. For example, organic additives or inhibitors were introduced to upgrade the corrosion protection properties of hybrid films [11]. Functional polyvinyl butyral (PVB) was merged into the sol-gel film to covalently (Si-O-C) bond with the inorganic matrix. The composite film obtained showed improved thickness and was free of cracks [12]. Inorganic metal salt additives, such as Ce(CH 3 COO) 3 , could bestow hybrid coatings with a self-healing property and enhance their corrosion inhibition ability due to the acceleration of the hydrolysis and condensation processes [13]. Corrosion-resistant inorganic microflakes, such as glass flakes, were also utilized to improve the anti-corrosion property of the sol-gel coatings due to their efficient barriers against corrosive intrusion and the extended diffusion path of the corrosives. However, the incorporation of nanoparticles and inhibitors sometimes increased the coating instability and reduced the sol-gel film's uniformity due to additive incompatibility and aggregation [14].
With oxygen functional groups (such as -OH, -COOH) on its basal planes and edges, graphene oxide (GO) has been drawing wide attention in coating applications [15]. Moreover, the functional groups of GO provide its good compatibility with the matrices and GO additives. Additionally, GO has a high aspect-ratio flake-like structure and thus has an excellent barrier property [5].
Hence, having splendid physical and chemical properties, graphene oxide (GO) has been extensively explored as an excellent additive to mediate the structures and the properties of coating films [16]. For example, Li et al. [17] reported that when GO was incorporated in poly(vinyl alcohol) (PVA) matrix as an additive, forceful interfacial interactions could be established between the GO and PVA through hydrogen bonding, leading to structural change and improved crystallinity of the PVA/GO nanocomposites. Xue et al. [15] by sol-gel method to make Go modified coating, it was prepared on aluminum alloy. The results demonstrated that GO can be covalently functionalized with silanol from silane coupling agents. The corrosion protective properties of sol-gel film distinctly by providing the good barrier property of layered GO and enhancing the cross-linking density of the film when the concentration of GO is 0.5 mg mL −1 .
It is well known that the spherical surfaces of colloid particles can be fabricated smoothly with polymeric coating films through the polymerization of small molecules by taking advantage of the electrostatic interaction [18]. Kang et al. [19] by layer-by-layer (LBL) assembly, the rG-o multilayers were successfully fabricated and transferred to Fe and Cu foils. The results mean that the rG-O layers play a role as a diffusion barrier of gas. The solution process using rG-O was easy and reproducible. Similarly, the surface of colloid microspheres can be homogeneously coated with GO through electrostatic interaction. We envisioned that these properties and techniques could be utilized to renovate the solgel coating structure and boost the corrosion protection capabilities of sol-gel composite coating films.
Herein, a feasible strategy to ameliorate the sol-gel coating structure through GO is presented. Shown in Scheme 1a-c are positively charged sol particles, GO, sol-gel/GO film magnified schematic diagram, respectively. The Scheme 1d show the synthesis schematic diagram of sol-gel, positively charged sol particles and negatively charged GO evenly mixed to obtain the coating and both the electrostatic interaction and the bonding be-tween GO and sol are employed to regulate the structure of the coating. Firstly, through adjusting the pH of silica sol particles, which are prepared positively charged silica sol particles. Then the positively charged sol particles is mixed with negatively charged graphene, and the silica sol particles around GO gathers and bonds to GO, forming lamellar structure with similar morphology to GO. In the meantime, the introduction of negatively charged GO also prompts the gelation of the positively charged silica sol to form a stratified structure of hybrid sol-gel/GO film.
In this work, tetraethoxysilane (TEOS) was used as a precursor to prepare the sol solution. Home-made GO was used for the gelation process and incorporated into the sol-gel film. The results showed that the incorporated GO can covalently bond with the sol particles and form a robust heterojunction and also induce the formation of a stratified structure. Electrochemical measurements showed that the resulting sol-gel/GO hybrid achieved through this novel strategy demonstrated a greatly enhanced corrosion protection capability. The regulating mechanism of GO on the gelation process to form the stratified structure is explored in the current research. In this work, tetraethoxysilane (TEOS) was used as a precursor to prepare the sol solution. Home-made GO was used for the gelation process and incorporated into the solgel film. The results showed that the incorporated GO can covalently bond with the sol particles and form a robust heterojunction and also induce the formation of a stratified structure. Electrochemical measurements showed that the resulting sol-gel/GO hybrid achieved through this novel strategy demonstrated a greatly enhanced corrosion protection capability. The regulating mechanism of GO on the gelation process to form the stratified structure is explored in the current research.

Pretreatment of Aluminum Alloy
AA5052 aluminum alloy samples (chemical composition shown in Table 1) were used. The samples were ground using diamond waterproof sandpaper to 2000 grit and cleaned in acetone (10 min) and ethanol (5 min) at 25 °C under ultrasonic irradiation. Then the samples were blow-dried with warm air after cleaning with deionized water. The powder was scraped from sol-gel film samples for transmission electron microscopy (TEM) observation.

Synthesis of Graphene and Sol-Gel Film
GO was prepared using the modified Hummers method [21]. To the suspension of 2 g graphite powder (Aladdin graphite powder, universal grade, 5000 mesh, 99.9995%, Shanghai, China) in 46 mL sulfuric acid (98 wt.%), 1.0 g of sodium nitrate was added with stirring at 0 °C. Next, 6.0 g potassium permanganate was added portion-wise under vigorous stirring at 10 °C. The mixture was maintained below 15 °C for 30 min and then maintained below 35 °C for 6 h. The solution was diluted with 100 mL deionized water, then underwent calefaction at 100 °C in a bain-marie for 1 h. The solution was then diluted to 240 mL with deionized water, followed by the addition of 10 mL 30% hydrogen peroxide. The solution was centrifuged at 8000 rpm and the obtained product was washed with 5 wt.% HCl and water for 3 times, respectively. Dialysis was performed to further remove impurities. Finally, the mixture was aired at 60 °C for 12 h in a dryer, resulting in GO as a brown powder.

Pretreatment of Aluminum Alloy
AA5052 aluminum alloy samples (chemical composition shown in Table 1) were used. The samples were ground using diamond waterproof sandpaper to 2000 grit and cleaned in acetone (10 min) and ethanol (5 min) at 25 • C under ultrasonic irradiation. Then the samples were blow-dried with warm air after cleaning with deionized water. The powder was scraped from sol-gel film samples for transmission electron microscopy (TEM) observation.

Synthesis of Graphene and Sol-Gel Film
GO was prepared using the modified Hummers method [21]. To the suspension of 2 g graphite powder (Aladdin graphite powder, universal grade, 5000 mesh, 99.9995%, Shanghai, China) in 46 mL sulfuric acid (98 wt.%), 1.0 g of sodium nitrate was added with stirring at 0 • C. Next, 6.0 g potassium permanganate was added portion-wise under vigorous stirring at 10 • C. The mixture was maintained below 15 • C for 30 min and then maintained below 35 • C for 6 h. The solution was diluted with 100 mL deionized water, then underwent calefaction at 100 • C in a bain-marie for 1 h. The solution was then diluted to 240 mL with deionized water, followed by the addition of 10 mL 30% hydrogen peroxide. The solution was centrifuged at 8000 rpm and the obtained product was washed with 5 wt.% HCl and water for 3 times, respectively. Dialysis was performed to further remove impurities. Finally, the mixture was aired at 60 • C for 12 h in a dryer, resulting in GO as a brown powder.
The sol solution was obtained by mixing 10 mL tetraethoxysilance (TEOS) and 20 mL ethanol and 10 mL deionized water. Then, the pH of the mixture was adjusted to 1 with acetic acid. The mixture was then stirred for 5 h and held for 48 h at 25 • C for complete hydrolysis (the zeta potential of the sol solution was determined to be +5 mV). An amount of 20 mg graphene oxide was added to 3 mL deionized water and sonicated for 3 h (the zeta potential of the suspension was −6 mV after the pH of the solution was adjusted to 1), and the resulting suspension was added to the afore-obtained sol solution to yield the sol-gel/GO composite with a concentration of 0.5 mg/mL. Sol solution without GO was synthesized as a control sample. The pre-treated sample were immersed into sol solution for 2 min, then taken out at the speed of 5 cm/min. The coated samples were heat-treated first at 60 • C for 80 min, then at 90 • C for 40 min and last at 150 • C for 10 min in the oven, and the obtained sol-gel films were designated as SG film and SG/GO film.

Characterization Techniques
A scanning electron microscope (SEM, JSM-7800F, JEOL, Tokyo, Japan) was used to observe the surface morphology of the samples. The microstructure of the samples was studied by transmission electron microscopy (HR-TEM, JEM-2100F, JEOL, Tokyo, Japan) equipped with an energy-dispersive X-ray spectrometer (EDX). The TEM samples were peeled from the samples. Raman spectra were performed by exciting a 633 nm wavelength He-Ne laser beam on the sample (confocal Raman), and the power of the laser was set at a minimum (6 mW). The position of the sample to be studied was focused by magnifying the microscope by 50 times. The zeta potential was measured by a Zetasizer Nano (ZS90, Malvern Instruments, Malvern, UK). The Raman spectra were recorded in the wave number range of 1000-2000 cm −1 . Electrochemical measurements (electrochemical impedance spectroscopy, polarization curve measurements) were performed with an electrochemical workstation (Interface 1000, Gamry, Philadelphia, PA, USA) in 3.5 wt.% NaCl solution. Polarization curve measurements were tested by sweeping the potential from −0.1 V to 0.1 V (vs. open-circuit potential) at a scan rate of 0.1667 mV/s, and fitted by the fitting tool (nonlinear fitting in a weakly polarized region) provided by the electrochemical workstation. With a sinusoidal perturbation of 5 mV, EIS measurements were conducted at open-circuit potential in the amplitude and a frequency domain from 10 5 Hz to 10 −2 Hz after 1 h, 72 h, 480 h and 720 h of immersion time. Zview software (V3.3a) was employed to analyze the impedance data. All the potentials were recorded in relation to the saturated calomel electrode (SCE). All tests were performed at room temperature.

Chemical Characterization of GO, SG Film and SG/GO Film
The Raman spectra of the GO, SG film and SG/GO film are presented in Figure 1. The Raman spectrum of the SG film has no peak, but two obvious peaks are observed in the spectra of the GO and SG/GO film. Generally, the Raman spectrum of GO exhibits a D band corresponding to defects inherent in the graphite oxide at 1351 cm −1 and a G band which is ascribed to the first-order scattering of the E 2g vibration mode at 1597 cm −1 [22]. The intensity ratio of the D band and G band was 0.935, while that of the SG/GO film was increased to 1.112, which is related to the decrease in size of the in-plane sp 2 area caused by repercussion between sol particles and GO. It is confirmed that a bond is formed between the GO and silica particles [22,23].  Figure 2a) is smooth from the cross-section and the complete cluster structure does not show any preferential orientation. Based on the SEM image in Figure 2b, a stratified structure with folded edges is formed with the incorporation of GO, and the thickness of the stratified structure is much thicker than that of the graphene oxide layer. Moreover, the SG/GO film exhibits a hierarchical structure characteristic. Figure 2c presents the TEM image of the SG film, which exhibits a uniform gel structure. However, for the SG/GO film (as shown in Figure 2e), stratified structures with uniform dispersion can be observed clearly. The main components in the SG film are silicon and oxygen according to the results of the EDS image (as shown in Figure 2d). Figure 2f corroborates that the observed SG/GO film is composed of GO with the presence of carbon elements.

Microstructure of SG Film and SG/GO Film
The differences between the SG film and SG/GO film may be elucidated by the influence of GO on the gelation process of the sol particles owing to its bearing oxygen functional groups on its edges' proximal planes, and negatively charged GO electrostatically attracted positively charged sol particles in solution. From this point of view, the negative electric field generated by GO regulates the polycondensation reaction of the surrounding sol particles, and controls the local particle alignment, so the sol-gel film finally forms a stratified structure similar to the shape of GO via electrostatic attraction and the bond relationship. This hybrid sol-gel film with a stratified structure is expected to demonstrate excellent corrosion protection performance.

Corrosion Protection Performance of Bare Al with SG Film and SG/GO Film
The potentiodynamic curves of the bare Al-alloy sample are presented in Figure 3, with SG film and SG/GO film coated specimens after 1 h of immersion in 3.5 wt.% NaCl solution.
Meanwhile, Table 2. lists the fitting results of the derived parameters of the polarization curves. Both the anodic and cathodic responses are significantly influenced by the added GO. The cathodic Tafel slopes (-β c ) of the SG/GO film show larger values compared to those of the SG film, and the decrease of the cathodic Tafel slopes of the SG/GO film coated samples indicates that the oxygen reduction reaction (O 2 + 2 H 2 O + 4 e → 4 OH − ) on the alloy is effectively reduced by the SG/GO film. It is clearly seen that the anodic Tafel slopes (β a ) of the SG/GO film coated sample are larger than those on the bare Al-alloy sample and SG film coated samples. The results illustrate that the anodic dissolution process (Al→Al 3+ + 3e) was weakened for the SG/GO film. In the whole polarization curve, it seems that both the anodic and cathodic current densities of the SG/GO film coated sample drop significantly compared with the SG film coated sample. The corrosion current density (j corr ) of the SG/GO film specimen was about 30 times less than that of the SG film coated sample. The incorporation of graphene oxide decreases the corrosion current density from 1.43 × 10 −7 A/cm 2 to 4.62 × 10 −9 A/cm 2 . Previous studies attributed these effects to a good barrier property from GO layered [22]. However, for this study, the result may be attributed to the stratified structure controlled by the GO in the coating, which prolongs the diffusion path of the depolarizing agent and aggressive ions. The formation of a stratified structure in the coating inhibits the occurrence and deterioration of corrosion, while increasing the crosslink density of the film to obtain a dense coating. Meanwhile, the stratified structure still maintains its bonding with the sol-gel matrix, which further enhances the compactness of the coating without cracks.  Figure 2 shows SEM and TEM images of the SG film and SG/GO film. The SG film (as shown in Figure 2a) is smooth from the cross-section and the complete cluster structure does not show any preferential orientation. Based on the SEM image in Figure 2b, a stratified structure with folded edges is formed with the incorporation of GO, and the thickness of the stratified structure is much thicker than that of the graphene oxide layer. Moreover, the SG/GO film exhibits a hierarchical structure characteristic. Figure 2c   The differences between the SG film and SG/GO film may be elucidated by the influence of GO on the gelation process of the sol particles owing to its bearing oxygen functional groups on its edges' proximal planes, and negatively charged GO electrostatically attracted positively charged sol particles in solution. From this point of view, the negative electric field generated by GO regulates the polycondensation reaction of the surrounding sol particles, and controls the local particle alignment, so the sol-gel film finally forms a stratified structure similar to the shape of GO via electrostatic attraction and the bond relationship. This hybrid sol-gel film with a stratified structure is expected to demonstrate excellent corrosion protection performance.  Meanwhile, the surface morphology differed after 1 h, 72 h, 480 h and 720 h. Samples are presented in Figure 5.

Corrosion Protection Performance of Bare Al with SG Film and SG/GO Film
The log|Z| vs. logf diagram of the SG/GO film and SG film coated samples shows higher impedance modulus values over all the frequency range compared with the bare Al sample. SEM images of the SG film and SG/GO film after a 1 h immersion in 3.5 wt.% NaCl solution show that the surface of both films still maintains its integrity, and no corrosion is visually observed on the surface (as shown in Figure 5a,e). At the same time, the |Z| 0.01Hz value (about 1.28 × 10 6 Ohm cm 2 ) of the SG/GO film coated sample is higher than the value (about 6.79 × 10 5 Ohm cm 2 ) of the SG film coated sample. The corrosion protection performance of the sol-gel film was reflected at a low frequency impedance value [24]. In the Bode plots it exhibits three time constant (see Figure 4a,b), which are located in the higher frequency (10 3 -10 5 Hz), the middle frequency (10 2 -10 0 Hz) and lower frequency (below 10 −1 Hz). In the lower frequency it partially overlaps with the peak at the middle frequency, which is related to the intermediate layer and the electrochemical reaction of the matrix [25,26].
After 72 h immersion, the high frequency response peak (10 3 -10 5 Hz) of the SG film coated sample has almost disappeared from the phase angle spectra (shown in Figure 4d). However, the peak at high frequency of the SG/GO film can still be observed clearly. In terms of the peaks at the middle and low frequency, it is clearly observed that the peak at the low frequency of the SG film and SG/GO film overlap partially with the peak at the middle frequency, and the peaks of the SG/GO film at the middle frequency and low frequency remain the same after 72 h immersion. This means that the substrate is not corroded. Moreover, the films still keep a complete surface according to the surface micrograph obtained (Figure 5f). However, for the SG film, as the immersion time increases, the peak at the middle frequency shows a conversion toward higher frequency. Meanwhile, the peak at low frequency shows a shift to the lower frequencies, indicating that the corrosion protection performance of the SG film is reducing and the substrate is beginning to corrode. Many cracks caused by corrosion products appear on the surface of the SG film (as presented in Figure 5b). With prolonged immersion time, the peak at high frequency shows a continuous decrease after 480 h, the peak at the middle frequency of the SG/GO film shows a shift toward higher frequency and the lower frequency peak shows a shift toward lower frequencies. Figure 5g presents the surface of the sample coated with SG/GO film after 480 h immersion. Peeling of the exfoliated stratified structure occurs on the surface of the substrate, which suggests damage to the SG/GO film. The integrity of the SG/GO film was damaged and the protection performance of the coating reduced. At the same time, the accumulation of corrosion products lead to more cracks on the surface of the SG film (as shown in Figure 5c). After 720 h of immersion (see Figure 4g,h), the peak at high frequency of the SG/GO film coated sample disappears substantially from the spectra. Only the middle and low frequency time constants appeared on the phase angle diagram, which suggests failure of the SG/GO film after 720 h immersion. Visible cracks appear on the surface of the SG/GO film (as shown in Figure 5h). In comparison, for the SG film (as shown in Figure 5d), more severe corrosion emerges on the surface of the SG film coated specimen in contrast with the SG/GO film coated samples. Meanwhile, comparing the surface states of these two coatings, it is easy to see that the destruction processes of the SG film and the SG/GO film are different. Figure 5c shows the SEM image of the SG film after 480 h immersion, from which film delamination and film cracking can be observed. Because the SG film has a rich porosity and brittle nature, the tensile stresses caused by corrosion products cause the SG film to crack. In conclusion, an exfoliated stratified structure can be observed on the SG/GO film (as shown in Figure 5g). The difference between the SG film and SG/GO film is that the stratified structures in the film reduce the damage of the coating by the lateral tensile stress, which avoids cracks in the coating. At the same time, the vertical tensile stress causes the stratified structure to peel from the coating, which damages the SG/GO film. The equivalent electric circuit (EEC) applied for numerical fitting of the EIS data is shown in Figure 6.
By the EEC it is possible to adequately fit the EIS curves of the bare Al sample with a two time constant (as shown in Figure 6a). Meanwhile, the EEC in Figure 6b was applied for the sol-gel coated specimen. The R sol corresponds to the solution resistance. R coat and Q coat were assigned to the resistance and constant phase element relating to the capacitances of the sol-gel, and R int and Q int are related to the resistance and capacitances of the intermediate layer. The charge transfer resistance and the double layer capacitance seemed to be related with the R ct and Q dl . Figure 6c was applied for the sol-gel film coated sample with the time unaltered in relation to the SG film. The derived parameters are listed in Table 3.  Meanwhile, Table 2. lists the fitting results of the derived parameters of the polarization curves. Both the anodic and cathodic responses are significantly influenced by the added GO. The cathodic Tafel slopes (-βc) of the SG/GO film show larger values compared to those of the SG film, and the decrease of the cathodic Tafel slopes of the SG/GO film coated samples indicates that the oxygen reduction reaction (O2 + 2 H2O + 4 e → 4 OH − ) on the alloy is effectively reduced by the SG/GO film. It is clearly seen that the anodic Tafel slopes (βa) of the SG/GO film coated sample are larger than those on the bare Al-alloy sample and SG film coated samples. The results illustrate that the anodic dissolution process (Al→Al 3+ + 3e) was weakened for the SG/GO film. In the whole polarization curve, it seems that both the anodic and cathodic current densities of the SG/GO film coated sample drop significantly compared with the SG film coated sample. The corrosion current density (jcorr) of the SG/GO film specimen was about 30 times less than that of the SG film coated sample. The incorporation of graphene oxide decreases the corrosion current density from 1.43 × 10 −7 A/cm 2 to 4.62 × 10 −9 A/cm 2 . Previous studies attributed these effects to a good barrier property from GO layered [22]. However, for this study, the result may be attributed to the stratified structure controlled by the GO in the The corrosion protection performance can be evaluated through the value of R coat . At the initial immersion, the R coat value of the SG/GO film is much higher than that of the SG film. The R coat values of the SG film decrease significantly and tend to disappear after immersing for 72 h, indicating that a large number of pores and cracks are formed on the sol-gel layer. In comparison, the R coat of the SG/GO film decreases more slowly with immersion time and remains relatively high even after immersion of 480 h, which indicates the slower formation of cracks in the SG/GO film and the excellent coating barrier performance. The Q coat of the SG film and SG/GO film increases during the immersion tests due to the increase of the dielectric constant for water absorption. Furthermore, the Q coat of the SG/GO film still exhibits a lower value even after a long immersion time. The above analysis indicates that the accretion of GO has a positive influence on the corrosion protection performance of the sol-gel film, which is attributed to the shape of the stratified structure that develops, with a higher cross-link density of the sol-gel film.   The log|Z| vs. logf diagram of the SG/GO film and SG film coated samples shows higher impedance modulus values over all the frequency range compared with the bare Al sample. SEM images of the SG film and SG/GO film after a 1 h immersion in 3.5 wt.% NaCl solution show that the surface of both films still maintains its integrity, and no corrosion is visually observed on the surface (as shown in Figure 5a,e). At the same time, the |Z|0.01Hz value (about 1.28 × 10 6 Ohm·cm 2 ) of the SG/GO film coated sample is higher than the value (about 6.79 × 10 5 Ohm·cm 2 ) of the SG film coated sample. The corrosion protection performance of the sol-gel film was reflected at a low frequency impedance value [24]. In the Bode plots it exhibits three time constant (see Figure 4a,b), which are located in the higher frequency (10 3 -10 5 Hz), the middle frequency (10 2 -10 0 Hz) and lower frequency (below 10 −1 Hz). In the lower frequency it partially overlaps with the peak at the middle frequency, which is related to the intermediate layer and the electrochemical reaction of the matrix [25,26].
After 72 h immersion, the high frequency response peak (10 3 -10 5 Hz) of the SG film coated sample has almost disappeared from the phase angle spectra (shown in Figure 4d). However, the peak at high frequency of the SG/GO film can still be observed clearly. In terms of the peaks at the middle and low frequency, it is clearly observed that the peak at the low frequency of the SG film and SG/GO film overlap partially with the peak at the middle frequency, and the peaks of the SG/GO film at the middle frequency and low frequency remain the same after 72 h immersion. This means that the substrate is not corroded. Moreover, the films still keep a complete surface according to the surface micrograph obtained (Figure 5f). However, for the SG film, as the immersion time increases, the peak at the middle frequency shows a conversion toward higher frequency. Meanwhile, the peak at low frequency shows a shift to the lower frequencies, indicating that the corrosion protection performance of the SG film is reducing and the substrate is beginning to corrode. Many cracks caused by corrosion products appear on the surface of the SG film (as presented in Figure 5b). With prolonged immersion time, the peak at high frequency shows a continuous decrease after 480 h, the peak at the middle frequency of the SG/GO film shows a shift toward higher frequency and the lower frequency peak shows a shift toward lower frequencies. Figure 5g presents the surface of the sample coated with SG/GO film after 480 h immersion. Peeling of the exfoliated stratified structure occurs on the surface of the substrate, which suggests damage to the SG/GO film. The integrity of the SG/GO film was damaged and the protection performance of the coating reduced. At the same time, the accumulation of corrosion products lead to more cracks on the surface of the SG film (as shown in Figure 5c). After 720 h of immersion (see Figure 4g,h), the peak at high frequency of the SG/GO film coated sample disappears substantially from the spectra. Only the middle and low frequency time constants appeared on the phase angle diagram, which suggests failure of the SG/GO film after 720 h immersion. Visible cracks appear on the surface of the SG/GO film (as shown in Figure  5h). In comparison, for the SG film (as shown in Figure 5d), more severe corrosion emerges on the surface of the SG film coated specimen in contrast with the SG/GO film coated samples. Meanwhile, comparing the surface states of these two coatings, it is easy to see that the destruction processes of the SG film and the SG/GO film are different. Figure 5c shows the SEM image of the SG film after 480 h immersion, from which film delamination and film cracking can be observed. Because the SG film has a rich porosity and brittle nature, the tensile stresses caused by corrosion products cause the SG film to crack. In conclusion, an exfoliated stratified structure can be observed on the SG/GO film (as shown in Figure 5g). The difference between the SG film and SG/GO film is that the stratified structures in the film reduce the damage of the coating by the lateral tensile stress, which avoids cracks in the coating. At the same time, the vertical tensile stress causes the stratified structure to peel from the coating, which damages the SG/GO film. The equivalent electric circuit (EEC) applied for numerical fitting of the EIS data is shown in Figure 6. By the EEC it is possible to adequately fit the EIS curves of the bare Al sample with a two time constant (as shown in Figure 6a). Meanwhile, the EEC in Figure 6b was applied for the sol-gel coated specimen. The Rsol corresponds to the solution resistance. Rcoat and The R int value of the SG/GO film is more than that of the SG film after 1 h of soaking. The SG/GO film specimen maintains higher R int values and lower Q int values after 480 h of immersion, which indicates that the intermediate layer still maintains good compactness and integrity. However, the SG/GO film shows a remarkable decrease of the R int value and increase of the Q int value after soaking for 72 h. This suggests the rapid failure of the SG film and the excellent protection properties of the SG/GO film even after successive immersion. Figure 7 shows the schematic illustration of the formation and corrosion protection mechanism of the SG/GO coating. The hydroxyl group at the edge of GO lamellar and the π-π bond of GO form p-π conjugated electron cloud [27], hence GO is electronegative as a whole and the Zeta potential of GO was tested to be −6 mV. The zeta potential of silica sol particles was +5 mV, which contained Si-OH groups. GO and silica sol were attracted to each other under electrostatic action. Hydroxyl of GO and silica sol were dehydrated and condensed. Silica sol groups are adsorbed by covalent bond around GO and layered SG/GO coating is formed under the guidance of GO. GO could block erosive ions and oxygen reaching the metal matrix [28]. The layered coating improved the crosslinking density and barrier properties, and effectively enhanced the corrosion resistance of SG/GO coating. This conclusion was consistent with our electrochemical test results.

Conclusions
Herein, a novel facile strategy was developed to promote the corrosion inhibition property of GO hybrid sol-gel coating (SG/GO film). By taking advantage of the different zeta potentials of GO and sol, GO was exploited as a regulator for the first time to regulate the sol-gel process and produce sol-gel films with a stratified structure. The sol particles are efficiently and densely cross-linked along the GO. Coating films were generated with reduced porosity and enhanced stability. The stratified microstructure inherited from the GO could efficiently extend the diffusion paths of the corrosives and thus improve the corrosion protection performance. Compared with traditional organic coatings, inorganic coatings had excellent weather resistance and environmental friendliness. After the introduction of GO, the advantages of inorganic coatings such as acid resistance and high salt resistance were increased. These advantages play an important role in metal protection, making the application range of metal wider and effectively improving The hydroxyl group at the edge of GO lamellar and the π-π bond of GO form pπ conjugated electron cloud [27], hence GO is electronegative as a whole and the Zeta potential of GO was tested to be −6 mV. The zeta potential of silica sol particles was +5 mV, which contained Si-OH groups. GO and silica sol were attracted to each other under electrostatic action. Hydroxyl of GO and silica sol were dehydrated and condensed. Silica sol groups are adsorbed by covalent bond around GO and layered SG/GO coating is formed under the guidance of GO. GO could block erosive ions and oxygen reaching the metal matrix [28]. The layered coating improved the crosslinking density and barrier properties, and effectively enhanced the corrosion resistance of SG/GO coating. This conclusion was consistent with our electrochemical test results.

Conclusions
Herein, a novel facile strategy was developed to promote the corrosion inhibition property of GO hybrid sol-gel coating (SG/GO film). By taking advantage of the different zeta potentials of GO and sol, GO was exploited as a regulator for the first time to regulate the sol-gel process and produce sol-gel films with a stratified structure. The sol particles are efficiently and densely cross-linked along the GO. Coating films were generated with reduced porosity and enhanced stability. The stratified microstructure inherited from the GO could efficiently extend the diffusion paths of the corrosives and thus improve the corrosion protection performance. Compared with traditional organic coatings, inorganic coatings had excellent weather resistance and environmental friendliness. After the introduction of GO, the advantages of inorganic coatings such as acid resistance and high salt resistance were increased. These advantages play an important role in metal protection, making the application range of metal wider and effectively improving economic benefits.

Data Availability Statement:
The data that support the findings of this study are available from the corresponding author upon reasonable request.