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Synthesis and Characterization of Epoxy-Rich TMOs Deposited on Stainless Steel for Corrosion Applications

Department of Electrical Engineering (SEES), Centro de Investigación y de Estudios Avanzados del Instituto Politécnico Nacional (CINVESTAV-IPN), Av. Instituto Politécnico Nacional 2508, Col. San Pedro Zacatenco, Mexico City 07360, Mexico
Department of Materials Science and Engineering, National Corrosion and Materials Reliability Laboratory, Texas A&M University, College Station, TX 77840, USA
Author to whom correspondence should be addressed.
Coatings 2022, 12(3), 387;
Submission received: 8 February 2022 / Revised: 4 March 2022 / Accepted: 9 March 2022 / Published: 15 March 2022
(This article belongs to the Special Issue New Anti-corrosion Coatings for Marine Materials)


Epoxy-trimetallic oxide (epoxy-TMO) coatings of ZrO2:TiO2:ZnO at different compositions were synthesized and used to protect a stainless steel surface. The different TMO compositions were synthesized using the ball-milling method and later dispersed on the polymer matrix. The different characterizations performed on these coatings showed that the epoxy-TMO coating with a ratio of 50:40:10 (wt%) exhibited the highest corrosion resistance, in the order of ~1012 Ωcm2, due to the barrier effect of the distributed particles after 28 days in an aggressive environment (3.5 wt% NaCl solution). The influence of the metal oxides in forming a semiconductor layer produces a capacitor-like behavior, influencing corrosion control via a mass transfer mechanism barrier. The water uptake reveals the effect of each metal oxide in the formation of a physical barrier due to the dispersion mechanism, as well as how the particles function within the polymer matrix.

1. Introduction

Stainless steel (SS) is widely used in industry due to its excellent corrosion resistance and low cost. However, this material tends to suffer localized corrosion due to the breakdown of the passivation layer formed on the steel surface [1]. Organic coatings are the most widely applied method for corrosion protection of metallic materials, providing a protective barrier and preventing the diffusion of oxygen and water through the insulating layer [2]. Among organic coatings, epoxy resins are the most used polymers in the protection of steel, due to their excellent physical and chemical properties—such as adhesion, chemical resistivity, and mechanical and dielectric properties [3]—and they are widely used for industrial applications such as aerospace parts, electrical laminates, and construction materials [4]. However, like all polymers, they are susceptible to corrosive species such as oxygen, aggressive ions, and water molecules at the metal-coating interface, reducing the coating adhesion and facilitating corrosion of the metal underneath the film [5,6]. However, incorporating inorganic nanoparticles can improve the barrier properties and protective performance of the epoxy coatings. Different inorganic materials, including silicon oxide (SiO2), titanium dioxide (TiO2), zinc oxide (ZnO), cerium oxide (CeO2), and zirconium oxide (ZrO2), among others, are recognized as excellent candidates for their physical and mechanical properties, owing to their grain size and grain boundary volume [7]. There are different types of applicator—such as brush, airbrush, doctor blade, drop- casting, dip-coating, spin-coating, etc.—for applying the epoxy coatings to the metallic surface [8].
Individual oxides of Zr, Zn, and Ti are commonly used for corrosion-resistant coatings, and present good performance. However, the use of single oxides exhibits some flaws, due to pores and cracks in the coatings. Conversely, a hybrid or mixed metal oxide coating can potentially combine the intrinsic properties of all of the metal oxides, improving the adherence and enhancing the barrier to dissemination and preclusion of charge transport. The properties of the coatings can be tailored by controlling the concentrations of each metal oxide nanoparticle to overcome the limitations of a single metal oxide [9,10].
This study proposes a novel and hybrid combination of ZrO2, TiO2, and ZnO nanoparticles at different ZrO2-richness ratios using the ball-milling technique, and added to a commercial epoxy resin intended to achieve anticorrosive properties. The extensive work was applied on a previously reported highly resistive TMO coating also synthesized via the ball-milling method. This synthesis method uses mechanical energy to activate chemical reactions and structural changes, and is able to reduce the particle size [11]. These TMO nanoparticles were deposited by RF magnetron sputtering as a multifunctional (self-healing, anticorrosive, antireflective, and self-cleaning) layer [12]. For the first time, we present a systematic fundamental analysis of the different nanoparticles’ ratios in the epoxy matrix, with a minimum wt%, in order to determine the efficacy in the corrosion protection properties on SS substrates.

2. Materials and Methods

2.1. Synthesis of the Trimetallic Oxide Compounds

The three different oxides (ZrO2, TiO2, and ZnO; Sigma-Aldrich, Mexico) were weighed and mixed at different enriched ZrO2 proportions, forming six different compositions of TMOs, as shown in Table 1. All of the mixed TMOs were annealed at 700 °C for 2 h in a non-vacuum oven and mechanically milled at 300 rpm for 3 h. Finally, the TMO nanocomposites were sintered at 700 °C for 2 h in order to increase the density of the different oxides and the formation of the metalloids [13].
The epoxy-TMO coatings were prepared using commercial epoxy resin (Grupo Imperquimia, Mexico City, Mexico) mixed with the different TMO compositions at proportions of epoxy resin at 99 wt% and TMO at 1 wt%, using magnetic stirring for 15 min. After that, the commercial hardener was added to the mixture to obtain a 60:40 wt% ratio of epoxy-catalyst mixed by magnetic stirring for 3 min and sonicated in deionized water to release trapped air bubbles inside the coating. The resulting epoxy-TMO coatings were deposited on the SS 430 metallic substrates by drop-casting, repeating this procedure to obtain uniform coatings controlled by a doctor blade, with average wet thicknesses of 100 µm. After that, the resulting coatings were dried at room temperature for 24 h and measured with a thickness measurer, obtaining an average thickness of the coatings between 60 and 80 µm.

2.2. Characterization

The crystal structure of the synthesized TMOs was characterized by X-ray diffraction (XRD, Bruker, Massachusetts, United States) with a copper Kα radiation source (λ = 1.5405 Å), at a scan rate of 0.04° min−1, using a Bruker AXS D8 Advanced apparatus. The oxides were analyzed in the 2θ range from 10° to 80°. The morphology and composition of the TMOs were studied using a TESCAN Vega3 SEM (TESCAN Company, Brno, Czech Republic) fitted with a Bruker EDS and an Olympus America DXS 500 optical microscope. Raman analysis was performed using NT-MDT NTEGRA spectra, with a shift in the range of 300 to 3300 cm−1. The optical absorbance of the coated films was characterized using a JASCO V-670 spectrophotometer in the wavelength between 200 and 600 nm, and the water contact angle was measured using Data Physics (OCA 35, dataphysics instruments, Filderstad, Germany) with 4 µL of distilled water.
The electrochemical behavior of the coatings was assessed in a 3.5 wt% NaCl solution at room temperature for various immersion times (i.e., from 1 to 28 days). The measurements were performed with a potentiostat/galvanostat (Gamry Instruments REF600® potentiostat, Gamry Instruments, Warminster Pensilvania, United States). A typical three-electrode setup was used: the coated SS substrate as the working electrode, with an exposed area of 2.714 cm2, a saturated calomel electrode (SCE) as the reference electrode, and a platinum grid wire as a counter electrode. Electrochemical techniques such as open-circuit potential (EOCP), electrochemical impedance spectroscopy (EIS), and linear polarization resistance (LPR) were performed using a Gamry REF600® potentiostat. EIS measurements were carried out at EOCP with a sinusoidal potential of 10 mV in amplitude. The frequency range was observed from 105 to 10−2 Hz, with 10 points per decade interval. The corrosion behavior of the commercial epoxy coating was also tested under the same conditions, providing a baseline for coating evaluation.

3. Results and Discussion

3.1. XRD

XRD patterns of TMO nanocomposites depict their polycrystalline nature, with a significant presence of multiple peaks corresponding to mixed metal oxide phases, indicating the metallization during the nanocomposite formation [12]. Figure 1 shows the XRD spectra of the TMO nanoparticles. The XRD results present the characteristic 2θ peak values at ~16.7°, 24.3°, and 43°, corresponding to the monoclinic phase of ZrO2, with the prominent peak at 2θ = 28.6° belonging to the (−111) plane (ICDD 00-065-0728) [14]. With an increase in the content of TiO2, the intensity of tetragonal anatase TiO2 (ICDD 01-070-2556) is enhanced, whereas the intensity of ZrO2 is reduced [15].
The observed peak at 2θ = 34.4° corresponding to the (002) plane suggests the presence of hexagonal ZnO (ICDD 01-082-9744) [16]. A small peak can also be found at a 2θ value of around 40°, corresponding to the (511) plane of the ZnZrO2, confirming the formation of the mixed metal oxide phase.
The average crystallite size (Table 2) for each oxide was calculated with the Debye-Scherrer equation, using diffraction angle and peak full width at half-maximum (FWHM):
D = 0.94 λ β c o s θ
where D is the crystallite’s average size, λ is the wavelength of the X-ray radiation, β is the peak FWHM in radians, and θ is the diffraction peak position.
The crystallite sizes of ZrO2 varied between 12 and 27 nm, depending on the content of the entire composite, as shown in Table 2. The crystallite size of ZrO2 for samples A to C was smaller than for samples D and E. This result shows that decreasing the quantity of ZrO2 in the TMO composite enhances the crystallinity of the nanoparticles. The average crystallite size varied between 35 and 44 nm for the ZrTiO4, indicating enhancement in crystallinity with increasing TiO2 content in the composite. The crystallinity of ZnZrO2 does not depend on the quantity of ZrO2, as was verified by the constant crystallite size of composite ZnZrO2 for all of the samples.

3.2. Morphological Characterization

The SEM micrograph of the TMO powders shows agglomeration of the nanoparticles with a random distribution of the constituent elements, with a grain size ranging between 130 and 500 nm; this could be due to the annealing process after the ball-milling synthesis provoking the increase in the particle size of the TMOs [17] (Figure 2a). Velumani et al. [12] synthesized this TMO via ball-milling and obtained an average grain size between 92 and 106 nm with decreasing ZrO2 content, including the formation of agglomerates. Figure 2b shows a micrograph where the thickness of the epoxy sample measured from the cross-section was ~70 µm, with no observation of significant agglomeration of the TMO nanoparticles within the epoxy coating.
The elemental composition of the epoxy-TMO coatings is shown in Table 3. The proportion between the epoxy coating and the TMO was small, and it was not possible to observe in the elemental mapping. We also observed that elements such as iron (Fe) and chromium (Cr) may correspond to the substrate and the content of carbon content from the epoxy material.

3.3. Raman Analysis

Figure 3 shows Raman analysis of the epoxy-TMO to determine whether the phases (wurtzite ZnO and monoclinic ZrO2) characterized by XRD as being present in the coatings maintain their phases after annealing at 700 °C [18]. The observed peaks at 1120 and 1620 cm−1 correspond to the benzene ring quadrant stretching characteristics of the epoxy ring vibration; the signal at 830 cm−1 could also be related to the vibrations of the entire epoxy ring (i.e., characteristic of the CH2 epoxy asymmetric, and vibration of the C-H groups of the epoxy ring) [19]. The absence of peaks of TMO oxides (1 wt%) may be due to their small amount, which is insufficient to exhibit significant peaks in the Raman modes corresponding to the present oxides.

3.4. Optical Analysis of Epoxy-Rich Coatings

The epoxy systems have significant chemical and mechanical properties; they possess aromatic groups with strong absorption in the UV range at 300 nm, making the epoxy structures susceptible to photodegradation. UV light forms free radicals on the surface of the polymer, and is highly active in attacking the polymer structures. Other environmental factors—including humidity, oxygen, temperature, and pollutants—can decrease the lifetime of the polymer. Thus, added inorganic nanoparticles such as ZnO and TiO2 scatter the light, and have broad absorption in the UV range, while they have almost no absorption in the visible range [20]. The absorbance and transmittance plots for the coatings (Figure 4) showed two characteristic absorption peaks of the epoxy resin at ~280 and ~350 nm.
The epoxy systems have significant chemical and mechanical properties. From the transmittance plot, it can be seen that they possess aromatic groups with strong absorption. All of the coatings presented low transmittance, reaching a maximum of 50%, showing the capacity of the coating to absorb light due to the properties of the different oxides in the TMOs. Incorporating TiO2 nanoparticles within the epoxy coating tends to broaden the absorption region of the epoxy resin and enhance the absorption intensity at around 250 nm within the TiO2 absorption range. Thus, the UV range is enhanced by incorporating this oxide, as observed in Figure 4 for the deposited coatings [21]. This enhancement may be due to TiO2, which has a wide bandgap of ~3.2 eV, and tends to absorb the shorter wavelength with high energy to excite its electrons below 400 nm, where it does not have a specific peak within this region. The absorption range of nano-ZnO reported between 360–230 nm can also block the UV radiation in organic coatings [22] and observed at ~246 nm.
Xu et al. [23] reported that TiO2/ZnO composites presented stronger photoabsorption than pure ZnO and TiO2. The absorption edge of TiO2/ZnO showed a redshift to the visible spectrum range, ascribed to better scattering of the induced electron-hole pairs in the porous architecture, as well as the mixture effect of the bandgap of the composite semiconductor improving the photoelectric effect of the composite films, and further enhancing the photocathodic properties of the stainless steel substrate.
ZrO2 presents excellent chemical and physical properties, with a wide bandgap larger than 5 eV, which is crucial in a luminescent material; its good optical transparency makes it a potential candidate for photocatalytic applications due to its high surface area and numerous oxygen vacancies. The monoclinic phase appears more stable at room temperature, depending on the different synthesis parameters, with a reported absorption signal ~204 nm [24]. In the epoxy-TMO, the signal is not observed within these ranges. The signal corresponding to an interaction between ZnO and ZrO2 is observed at ~246 nm, decreasing with the reduction in the ZrO2 ratio in the coatings. Sathyaseelan et al. [25] reported absorption peaks at 215 and 217 nm for synthesized and calcined samples of ZrO2 due to the Zr+4 ions’ d transition. The nanoparticles also showed a weak absorption band at 310 nm due to mid-gap trap sides, such as surface defects and oxygen vacancies. The surface modification resulted in a sharp increase in absorption by the ZrO2 within the visible region.

3.5. Contact Angle Measurement

Water contact angle (CA) measurements were carried out for the epoxy-TMO coatings to investigate the coated surfaces’ wettability state and determine the effects of the different oxides on the coated systems (Table 4). For the epoxy samples, it was not possible to determine a contact angle, and for the epoxy coatings with the nanoparticles, there were differences in the CA. However, the trend showed no significant variation of the contact angle with the decrease in ZrO2. All of the epoxy coatings presented hydrophilic characteristics close to 90° except for the epoxy-D coating, which presented a CA of ~73.8° and, compared to the other coatings, exhibited more hydrophilic characteristics. In comparison, the reported CA values for ZrO2 and ZnO were 67° and 75°, respectively [26].
For these epoxy-TMO coatings, there are two factors related to reducing the water contact angle: the first is the characteristics and properties of the trimetallic nanoparticles; the second is the surface roughness and porosity of the coating. ZrO2 has the property of increasing the contact angle, reducing the wettability of the material [27]. TiO2 shows a self-cleaning action related to its photocatalytic activity. The relationship between TiO2 and hydrophilicity is that the water molecules are chemisorbed on the TiO2 surface. These water molecules further absorb water via physisorption (van der Waals forces or hydrogen bonds). The physisorbed water molecules act as barriers to prevent close contact between the surface and pollutants. The combination of TiO2 with ZnO improves the hydrophilicity due to the formation of surface oxygen vacancies [28]. Sanu et al., further explained that reducing the contact angle can also reduce Ti+4 cations to a Ti+3 state, and oxidation of O2− anions expels some oxygen atoms. When the surface is exposed to moisture, the OH molecules are physisorbed to the vacancy sites, and the adsorbed OH groups on the surface can convert the surface into a hydrophilic one by creating a sheet of chemisorbed H2O through van der Waals forces that block the close contact between the surface and adsorbed contaminants. Thus, the dirt absorbed on the film’s surface can be quickly detached using water spread on the surface, showing a self-cleaning effect [29].

3.6. Electrochemical Characterization

EIS spectra illustrate the interfacial characterization over time based on the coating composition. Figure 5a–c display the three EIS signatures (Nyquist, Bode, and phase angle, respectively) for the epoxy and epoxy-TMO compositions following 21 days of 3.5 wt% NaCl, exposure where the representative values of this interface display high resistance.
The classic water uptake process occurring in a polymeric matrix coating [30] prevails during the early stages, achieving resistances in the order of 106–1011 Ωcm2. The semicircle or loop shape of the complex representation resembles the epoxy’s evolution in terms of typical charge transfer and capacitance due to the mentioned water uptake within the matrix. The coating has a finite impedance magnitude marked by the loop magnitude (~80 × 109 Ωcm2). For the epoxy-TMO coatings, epoxy-A illustrates a finite impedance magnitude, with a high magnitude. The complex representation shows capacitive characteristic mechanisms due to the electrolyte uptake; the TMO configuration 95:5:5 (ZrO2:TiO2:ZnO) confers barrier properties to the polymer matrix. Individually, each oxide provides corrosion protection. For instance, epoxy coatings with TiO2 nanocrystals at 1 wt% showed a maximum corrosion resistance of 104 Ωcm2 for these scratched coatings immersed for 18 days in 3.5 wt% NaCl [31]. Xavier J. et al. [32] synthesized epoxy-ZrO2 coatings at 10 wt% that, after 15 days of immersion in the same electrolyte, obtained a maximum resistance in the order of 105 Ωcm2. Finally, Rostami et al. [33] synthesized epoxy coatings with 4 wt% ZnO after exposure to the same aggressive environment for 30 days; after 30 days, the coating achieved a maximum resistance in the order of 108 Ωcm2. The results observed in the literature prove the efficiency of the combination of these three nanoparticles in improving the corrosion resistance of the coatings. It is well known that the addition of TiO2:ZrO2 permits the formation of a physical barrier. TiO2 is used in pigments to block electrolyte transport. With the addition of ZrO2, there is a reduction in the ionic species reaching the bulk of the polymer, where the particles are distributed in the polymer matrix [34,35].
A higher percentage of TiO2 gives similar properties to the previous epoxy composition. The epoxy-B formulation shows controlled water uptake with a capacitive-like behavior due to the higher impedance, similar to epoxy-A, with the phase angle in both cases (epoxy-A and -B) appearing identical, along with the frequency range. Epoxy-C contains no higher concentration of TiO2 and ZnO, but a decrease in the ZrO2 concentration. The results following 21 days present a change in the transport mechanism and an increase in the impedance magnitude. The Nyquist (or complex) plot (Figure 5a) presents a diffusion signature characteristic of the mass transport control process at low frequencies. The higher concentration of TiO2 influences the particle distribution within the matrix, as well as the transport mechanism.
From Figure 5a–c, the observed impedance data of the hybrid coatings were analyzed by fitting them to an equivalent circuit model used to yield information on the corrosion mechanism and/or corrosion rate. For these coatings, it is essential to note that the epoxy-D coating with a proportion of 50:40:10 (ZrO2:TiO2:ZnO) is the one with the highest resistance, reaching values close to 1012 Ωcm2, with an ideal capacitance behavior and an infinite real impedance as presented in the equivalent circuit proposed in Figure 6a, while the other epoxy-TMO coatings present the equivalent circuit shown in Figure 6b.
During the simulation, a constant-phase element (CPE) was used instead of an ideal capacitor to account for the deviations from ideal behavior. The impedance of a CPE (ZCPE) can be defined by ZCPE = (1/Y) (jω)η, where ω is frequency, Y is pseudo-capacitance, and η is associated with the system homogeneity; when this equation describes a capacitor, η = 1 and Y = C (capacitance).
The fitted data were acquired considering χ2 < 10−3, as observed in Table 5. This information suggests that, in the case of epoxy-D, there is a dielectric barrier blocking any water uptake and electrolyte drainage within the coating during the exposure time, as shown in the corrosion mechanism in Figure 7 The 40 wt% TiO2 influences the transport mechanisms within the polymeric coating layer. The formation of an ideal capacitor considers the distribution of particles favoring the physical barrier within the polymer matrix. The semiconductor properties due to the presence of TiO2 illustrate the blocking of the ionic species or any electrolytes within the polymer matrix.
The epoxy-TMO coatings presented good resistance behavior by assuming physical barrier protection due to the properties of ZrO2 that could present isolator and conductive behavior, and that with the interactions of TiO2 and ZnO, the coating presents an additional barrier by using the TiO2 particles as fillers and blockers. The particle distribution suggests a random distribution within the polymer matrix, and also at the coating surface. The contact angle is clear evidence of the influence of the distribution; TiO2 is present at the outmost surface, lowering the contact angle. The contact angle and resistance properties decrease with the increase in TiO2, wetting the surface and taking nothing into the matrix.
Epoxy-D shows a phase angle magnitude close to 90 degrees, while the frequency range and total impedance magnitude reached 1012 Ωcm2 after 21 days of exposure. The transition of interfacial mechanisms was evident with the increase in TiO2 particles, while ZrO2 decreased and ZnO remained constant. The 90:5:5 (ZrO2:TiO2:ZnO) ratio showed water uptake with the coating, displaying capacitance and a finite charge transfer process. The transition of interfacial mechanisms was evident with the increase in TiO2 particles, while ZrO2 decreased and ZnO remained constant. The increase in TiO2 in the oxide composition 65:25:10 (ZrO2:TiO2:ZnO) made the mechanism more diffusion-controlled. This was due to a barrier layer influenced by the TiO2 particles, and the lower conductivity as a result of decreasing ZrO2. Finally, the highest concentration of TiO2 (50:40:10, ZrO2:TiO2:ZnO) produced an ideal capacitance behavior. The particles formed a dielectric layer with no passage of electrolytes, producing an ideal capacitor.
Figure 8a,b present the optical images of the coatings after 28 days of immersion, comparing epoxy-A (Figure 8a) and epoxy-D (Figure 8b), where we can see damage to the interface of the steel substrate, while the epoxy-D does not show visual damage in either the coating or the interface.
Figure 7 presents the protection mechanism of the epoxy-D coating, where it is shown how the integration of the nanoparticles adds an additional barrier layer influencing the electrolyte transport. Mass transport is characteristic of the complex signature and the phase angle format at the lowest frequencies.
Table 6 shows the corrosion resistance rates for different coatings and the metallic substrate at day 21. We can see the decrease in the icorr with the increase in the TiO2 and ZnO and the decrease in ZrO2 content of the TMOs. We observed that the increase in the vcorr of epoxy-A was consistent with the results obtained in EIS, where the coatings epoxy-C and epoxy-D presented the lowest corrosion rates of 2.93 × 10−6 and 3.33 × 10−6 mpy, respectively.

4. Conclusions

TMOs of ZrO2:TiO2:ZnO were synthesized via the ball-milling method, and later incorporated into a commercial epoxy polymer (epoxy-TMO) by magnetic stirring and deposited on an SS substrate to reinforce the barrier properties in an aggressive environment of 3.5 wt% NaCl for 28 days. The different characterizations showed that epoxy-TMO coatings presented different UV absorbance, hydrophilic, and barrier properties, improving the properties of the epoxy coating due to the combination and synergy of the three oxides. After 21 days in the aggressive environment of 3.5 wt% NaCl, the epoxy-D coating, with a TMO composition of 50:40:10, not only showed higher hydrophilic properties, but also presented the highest resistance, in the order of ~1012 Ωcm2, with an almost capacitive behavior. Thus, the engineered composition of ZrO2:TiO2:ZnO (50:40:10 wt%) can be considered the ideal candidate for use in organic coatings to reinforce their barrier properties.

Author Contributions

Conceptualization, S.V.; methodology, S.V.; validation, S.V., A.F.-A. and H.C.; investigation, S.V., B.B.G., A.A. and G.R.; data curation, A.F.-A. and H.C.; writing—original draft preparation, A.F.-A.; writing—review and editing, A.F.-A., S.V. and H.C.; visualization, A.F.-A.; supervision, S.V. and H.C.; project administration, S.V.; funding acquisition, S.V. All authors have read and agreed to the published version of the manuscript.


Not applicable.

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

The raw/processed data required to reproduce these findings cannot be shared at this time, as they also form part of an ongoing study.


A.C. Ferrel-Alvarez, Brenda Galicia, A. Ashk, and G. Regmi wish to thank CONACyT for their postdoctoral and doctoral scholarships.

Conflicts of Interest

The authors declare no conflict of interest.


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Figure 1. XRD spectra of the sintered TMO (ZrO2:TiO2:ZnO) nanoparticles, ball-milled and annealed at 700 °C.
Figure 1. XRD spectra of the sintered TMO (ZrO2:TiO2:ZnO) nanoparticles, ball-milled and annealed at 700 °C.
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Figure 2. (a) SEM micrograph of TMO (ZrO2:TiO2:ZnO); (b) cross-section SEM images of epoxy-TMO coatings on an SS substrate.
Figure 2. (a) SEM micrograph of TMO (ZrO2:TiO2:ZnO); (b) cross-section SEM images of epoxy-TMO coatings on an SS substrate.
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Figure 3. Raman spectra of the epoxy-TMO coatings at different ratios of ZrO2:TiO2:ZnO. Epoxy-A (90:5:5), Epoxy-B (80:10:10), Epoxy-C (65:25:10), Epoxy-D (50:40:10), Epoxy-E (40:50:10).
Figure 3. Raman spectra of the epoxy-TMO coatings at different ratios of ZrO2:TiO2:ZnO. Epoxy-A (90:5:5), Epoxy-B (80:10:10), Epoxy-C (65:25:10), Epoxy-D (50:40:10), Epoxy-E (40:50:10).
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Figure 4. UV absorbance of the synthesized epoxy-TMO (ZrO2:TiO2:ZnO) coatings: Epoxy-A (90:5:5), Epoxy-B (80:10:10), Epoxy-C (65:25:10), Epoxy-D (50:40:10), Epoxy-E (40:50:10).
Figure 4. UV absorbance of the synthesized epoxy-TMO (ZrO2:TiO2:ZnO) coatings: Epoxy-A (90:5:5), Epoxy-B (80:10:10), Epoxy-C (65:25:10), Epoxy-D (50:40:10), Epoxy-E (40:50:10).
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Figure 5. (a) Nyquist, (b) Bode, and (c) phase angle plots of the epoxy and epoxy-TMO coatings at day 21.
Figure 5. (a) Nyquist, (b) Bode, and (c) phase angle plots of the epoxy and epoxy-TMO coatings at day 21.
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Figure 6. Electrochemical equivalent circuit proposed to model impedance data: (a) epoxy-D coating, and (b) other samples.
Figure 6. Electrochemical equivalent circuit proposed to model impedance data: (a) epoxy-D coating, and (b) other samples.
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Figure 7. Mechanism of corrosion protection of the epoxy-D coating.
Figure 7. Mechanism of corrosion protection of the epoxy-D coating.
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Figure 8. (a) Cross-section optical images of (a) epoxy-A and (b) epoxy-D.
Figure 8. (a) Cross-section optical images of (a) epoxy-A and (b) epoxy-D.
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Table 1. Composition of trimetallic oxides (wt%).
Table 1. Composition of trimetallic oxides (wt%).
Table 2. Average crystallite size of the TMO oxides.
Table 2. Average crystallite size of the TMO oxides.
Table 3. Elemental composition for a cross-section image of the epoxy films with different trimetallic oxide compositions.
Table 3. Elemental composition for a cross-section image of the epoxy films with different trimetallic oxide compositions.
Table 4. Contact angle measurements of epoxy-TMO coatings.
Table 4. Contact angle measurements of epoxy-TMO coatings.
SampleThickness (µm)Contact AngleDrop Image
Epoxy340NA Coatings 12 00387 i001
Epoxy-A270.885.7 ± 0.4 Coatings 12 00387 i002
Epoxy-B253.981.2 ± 0.3 Coatings 12 00387 i003
Epoxy-C271.284.6 ± 0.4 Coatings 12 00387 i004
Epoxy-D292.573.8 ± 0.3 Coatings 12 00387 i005
Epoxy-E302.681.9 ± 0.3 Coatings 12 00387 i006
Table 5. Electrochemical parameters extracted from impedance data for the epoxy and epoxy-TMO coatings immersed in 3.5 wt% NaCl solution for 21 days.
Table 5. Electrochemical parameters extracted from impedance data for the epoxy and epoxy-TMO coatings immersed in 3.5 wt% NaCl solution for 21 days.
SamplesRs (Ωcm2)Rcoat
(S * s^η)
(S * s^η)
Epoxy101.333.54 × 10677.92 × 10−120.94276.49 × 10−120.4988.43 × 1091.232 × 10−3
A32.6065.28327.5 × 10−90.811167.8 × 10−90.9343.2 × 106959.2 × 10−6
B1076.7739.44 × 10−90.867377.6 × 10−90.858211.2 × 106583.6 × 10−6
C1.14 × 1033.589 × 10962.55 × 10−120.984633.5 × 10−120.581169 × 109446.1 × 10−6
D1001.672 × 101269.84 × 10−121 699.5 × 10−6
E3.5748.2018.09 × 10−90.97785.8 × 10−90.894114.7 × 106205.4 × 10−6
* means S is multiplied (S)(s^η).
Table 6. Linear polarization resistance (LPR) of the coatings at 21 days.
Table 6. Linear polarization resistance (LPR) of the coatings at 21 days.
SS−0.23219.95 × 1031.306 × 10−6219.9 × 10−3
Epoxy−0.117938 × 10627.78 × 10−124.68 × 10−6
Epoxy-A0.15959.81 × 106435.6 × 10−1273.34 × 10−6
Epoxy-B0.12554.51 × 1064.77 × 10−1280.46 × 10−6
Epoxy-C−0.5571.498 × 10917.39 × 10−122.93 × 10−6
Epoxy-D−3.281.32 × 10919.79 × 10−123.33 × 10−6
Epoxy-E0.04340.36 × 106645.5 × 10−12108.7 × 10−6
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Ferrel-Alvarez, A.; Galicia, B.B.; Ashok, A.; Regmi, G.; Velumani, S.; Castaneda, H. Synthesis and Characterization of Epoxy-Rich TMOs Deposited on Stainless Steel for Corrosion Applications. Coatings 2022, 12, 387.

AMA Style

Ferrel-Alvarez A, Galicia BB, Ashok A, Regmi G, Velumani S, Castaneda H. Synthesis and Characterization of Epoxy-Rich TMOs Deposited on Stainless Steel for Corrosion Applications. Coatings. 2022; 12(3):387.

Chicago/Turabian Style

Ferrel-Alvarez, Atzin, Brenda B. Galicia, Adhikari Ashok, Ganesh Regmi, Subramaniam Velumani, and Homero Castaneda. 2022. "Synthesis and Characterization of Epoxy-Rich TMOs Deposited on Stainless Steel for Corrosion Applications" Coatings 12, no. 3: 387.

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