Novel highly efficient ternary ZnO wrapped PPy-NTs/g-C₃N₄ nanocomposite as an epoxy coating for corrosion protection

Abstract

The main goal of this study is to develop an epoxy coating coupled with an organic–inorganic hybrid nanocomposite that can be used as a corrosion-inhibiting pigment on carbon steel. Herein, polypyrrole nanotubes (PPy-NTs), polypyrrole nanotubes/g-C₃N₄ (PPy-NTs/g-C₃N₄) and novel nano-composite polypyrrole nanotubes/g-C₃N₄/ZnO (PGZ) were prepared by facile wet impregnation approach. The developed pigments were investigated using XRD, FTIR, FE-SEM equipped EDS. Electrochemical impedance spectroscopy (EIS) and polarization measurements were used to assess the behavior of the prepared pigments on the anticorrosion performance of epoxy resin coatings. EIS experiments revealed that introducing nano-pigments to neat coatings enhanced the epoxy resin and charge transfer resistance. The anticorrosion performance of the three nano-pigments was assessed as follows: PGZ ˃ PPy-NTs/g-C₃N₄˃ PPy-NTs.

Introduction

Metal corrosion represents an emergent problem when metal components undergo damage by chemical or electrochemical interactions. In the past few decades, organic coating developed as a highly effective approach for metal protection. Epoxy coating is one of metal anticorrosion technology's most established and operative methods. The benefits of waterborne epoxy coatings for industries include simplicity of application, lowering flammability and health risks when dealing with paint, less odor, simple washing with water in place of organic solvents, Excellent chemical inertness and good hydroxyl group adhesion to metallic surfaces^1–4. However, these coatings are hydrophilic, and corrosive ions could easily permeate through them. Additionally, the pores and flaws produced by the aqueous epoxy coatings' curing process may help corrosive chemicals diffuse into the coating. Because of this, even though aqueous epoxy coatings have been commercially available for more than 40 years, their usage is limited in corrosive environments, especially in marine environments^5–8.

Nanotechnology is a promising approach that can efficiently overcome these drawbacks, enhance barrier effectiveness of the aqueous epoxy coatings, and produce nanocomposite coatings with long-term corrosion resistance^9–11. For instance, polymeric nano-reinforced coatings have drawn much scientific attention as a practical way to protect metal surfaces from corrosion and fouling, particularly steel. Corrosion protection for bulky materials can be improved depending on the mechanical, physical, chemical features of materials in the nano-range¹². It will be possible to attain this good barrier performance by lowering porosity, zigzagging the diffusion pathway, and making nanoparticles soluble in the polymer matrix¹³.

Among the most often utilized inorganic nanoparticles, nano-zinc oxide serves various functions and is used to create multifunctional nano coatings^14–18. It has great dispersion with no aggregations, high hardness, a low refractive index, and hydrophobic enhancement^2,19–21. On the other hand, intrinsically conducting polymers (ICPs) have received much attention due to their numerous potential uses in water treatment, sensors, supercapacitor electrodes, biological industries, and corrosion prevention^22–26. ICPs can provide a barrier layer of protection and release coating inhibitors in the anticorrosion sector¹². Additionally, they can undergo redox processes and thereby allow for the binding and ejecting of counter-ions (dopants) in response to the variation of the metal surface potential stimulated by local electrochemical reactions due to the corrosion²⁷.

Polypyrrole (PPy) is the most promising polymer among the ICPs because of its simple polymerization, mechanical durability, improved biocompatibility, and tunable electrical properties¹³. The anticorrosion capabilities of the coatings are enhanced by selecting the right synthesis parameters^28–31.

Two-dimensional with sheet-like nanomaterials with, high specific surface areas, chemical constancy, and great mechanical strength, such as graphitic carbon nitride (g-C₃N₄) nanosheets, have been incorporated inside the polymer coatings as nanofillers to decrease the defects, increase barrier resistance, and enhance the mechanical performance of the coatings^32–34. Compared to graphene, the g-C₃N₄ is significantly more stable physic-chemically and contains a lot of nitrogen in the plane of the molecule. By possessing good mechanical stability and chemical resistance features, the reinforcement of g-C₃N₄ to a base epoxy matrix could greatly improve the mechanical strength of the final functionalized coating. In the past two years, some of the researchers are focused on their research to utilize the novel g-C₃N₄ as reinforcement materials for improving the overall performance of the polymer matrix composite materials^35–38.

Based on the abovementioned studies, a straightforward wet impregnation approach was applied to prepare highly efficient ZnO/PPy-NTs/g-C₃N₄ nanocomposite as a novel epoxy coating. The ZnO/PPy-NTs/g-C₃N₄ nanocomposites were thoroughly characterized, and their uniform distribution and structure were confirmed. Finally, the produced composite was further reinforced with epoxy coatings, and the corrosion-resistant performance of the developed nanocomposite/epoxy coating was methodically evaluated.

Experimental

Preparation of ZnO nanoparticles (ZnO NPs)

Zinc oxide nanoparticles are prepared by the sol–gel method. 0.5 g of Zinc acetate dihydrate was typically dissolved in 50 mL ultrapure water. Then, the NH₄OH solution dropped until pH 8 was reached, and the mixture kept stirring for 3 h until a white sol was formed. After aging the white sol for 48 h, the gelatinous phase was produced. Afterward, the gelatinous substance was dried at 100 °C. Finally, the dried powder was calcined at 500 °C for 2 h forming ZnO nanoparticles.

Preparation of polypyrrole nanotubes (PPy-NTs)

PPy-NTs were synthesized via the chemical oxidation polymerization technique by sodium bis(2-ethylhexyl) sulfosuccinate emulsions (AOT) reverse (water-in-oil) emulsions with minor modifications³⁹. Typically 0.7 wt% of PPy: FeCl₃ was added to the AOT reversed micelle phase and stirred for 1 h. Then the formed product was rinsed against ethanol and kept under vacuum drying. AOT reverse cylindrical micelles were employed as the soft template. When the product was washed thoroughly with excess ethanol, AOT and other residual reagents were removed, leaving the PPy-NTs.

Preparation of g-C₃N₄ nanosheets

The bulk g-C₃N₄ was prepared using thiourea as a starting material. 4 g of thiourea powder was typically thermally treated at 500 °C under Ar gas flow⁴⁰. For the preparation of g-C₃N₄ nanosheets, typically, 1 M HNO₃ and 2 g of bulk g-C₃N₄ were mixed and agitated for 24 h at 90 °C. After treatment, a uniformly mixed suspension was centrifuged to remove the supernatant. The residue was then rinsed twice with ultrapure water before being vacuum-dried for 24 h at 70 °C. It's significant to note that during the acidic treatment process, g-C₃N₄ sheets were oxidized and exfoliated by the entrance of HNO₃ particles between the interlayers, resulting in the oxidation of the C-N bonds of the triazine units and the introduction of oxygen-functional groups. The protonated g-C₃N₄ sheets were then further exposed to exfoliation by ultra-sonication in ultrapure water for 30 min. The resultant dispersion was subsequently centrifuged and thoroughly washed with ultrapure water and kept drying at70 °C.

Preparation of ternary ZnO/PPy-NTs/g-C₃N₄ hybrid nanocomposite (ZPG)

The straightforward wet impregnation approach was used to prepare ZnO/PPy-NTs/g-C₃N₄ nanocomposite (ZPG). Typically, 1:1:1 wt. % of ZnO:PPy-NTs:g-C₃N₄ are mixed with 50 mL methanol and then subjected to sonication for 2 h. After that, the suspension was stirred until the volatilization of methanol, and the product was kept dried at 60 °C. Finally, the schematic representation of the ternary ZnO/PPy-NTs/g-C₃N₄ hybrid nanocomposite (ZPG) fabrication procedure is displayed in Fig. 1.

Figure 1.

Schematic illustration of ternary ZnO/PPy-NTs/g-C₃N₄ fabrication procedure.

Characterization of the as-prepared materials

Field emission scanning electron microscopy (FE-SEM-Quanta-250 model) was used for morphology investigation. The chemical composition of the prepared samples was examined by X-ray diffraction (XRD-X’Pert Pro PANalytical model). Infrared spectroscopy investigates the function groups (IR-Perkin Elmer model). Examining oxidation states was done using an X-ray photoelectron (XPS-Thermo Fisher, Scientific model).

Preparation of the nanocomposite coatings

Acetone (a solvent) and hardener (resin/hardener with volume ratio = 2) are used to disperse 1.0% of as-prepared materials inside epoxy resin (Bisphenol epoxy resin- PC™ Resin 80–80% solid content) to create nanocomposite coatings. To achieve the required nanoparticle size, this mixture was stirred mechanically (speed = 1500 rpm) for 2.0 h, sonicated for 3 h, and then ground in a YLK Mini planetary ball mill for 3 h. Vacuum evaporation was used to remove the acetone. The clean substrate was coated with nanocomposite coatings using a film applicator. The coating micrometre (Mitutoyo.co) was used to measure the dry film thickness, which was 53 ± 2.3 μm. The hybrid composite concentration calculated during coating preparation based on the weight of the solid components present in the coating formulation. The volatile components, such as solvents or reactive diluents, are not considered in the calculation. The concentration is expressed as a percentage of the total weight of the dry components.

Electrochemical measurements

Electrochemical impedance spectroscopy (EIS) and polarization measurements were used to assess the anticorrosion characteristics of coatings made of nanocomposite materials. Three electrode cells and Gamry 3000 potentiostat/galvanostat were used to conduct the experiments. The electrode cell arrangement included a saturated calomel electrode (SCE, reference electrode), coated carbon steel (working electrode), and platinum (auxiliary electrode–surface area = 4.6 cm²). The composition of carbon steel is (wt. %): C(0.24%), P(0.028%), Mn(1.3%), Cr(0.26%), Cu (0.47%), Ni (0.28%), S(0.027%); Fe(balance%). The surface area of working electrode is 2.8 cm². Before applying coatings, the carbon steel samples were abraded with SiC sheet (grads = 500, 800, and 1200) and washed with acetone and a solution of distilled water. The EIS measurements were conducted at open circuit potential (OCP) with voltage amplitudes of 10 mV in the frequency range of 0.01 Hz to 100 kHz. For EIS data fitting, the EC-Lab program was utilized. Polarization curves were recorded in a voltage range of ± 250 mV vs. OCP at a constant sweep rate of 1.0 mV s⁻¹. The electrolyte is 3.5% NaCl solutions (pH = 7.8, conductivity = 52 mS cm⁻¹).

Results and discussions

Structural and morphological characteristics

The XRD patterns and FTIR spectra of ZnO, PPy-NTs, bulk g-C₃N₄, g-C₃N₄ nanosheets, and ternary ZPG nanocomposite are presented in Fig. 2a, b.

Figure 2.

(a) XRD pattern, and (b) FTIR spectra of PPy-NTS, bulk g-C₃N₄, g-C₃N₄ nanosheets, ZnO, ZPG hybrid nanocomposite.

Regarding the XRD pattern (Fig. 2a), PPy-NTs displayed an amorphous nature with a non-crystalline (wide) peak seen at roughly 2θ of 25°, displaying the distinctive properties of the matrix (Fig. 2a)^41–43. For bulk g-C₃N₄ (Fig. S1), two distinctive diffraction peaks were identified at 27.3° and 13.3°, respectively^40,44 These peaks are attributed to the (002) crystal faces of interlayer aromatic graphitic-like structures. Notably, the peak at 27.3° for g-C₃N₄ nanosheets (Fig. 2a) was slightly displaced to 27.6° compared to that of bulk g-C₃N₄ sheets, indicating a smaller interlayer spacing among the individual sheets that were initially formed^45,46. Additionally, due to the sharp reduction in the g-C₃N₄ layers' planar distance during protonation and exfoliation processes, the strength of the 13.3° peak for the nanosheets is less obvious and significantly reduced compared to that of bulk g-C₃N₄⁴⁵, displaying a single-layered structure. Concerning zinc oxide (Fig. 2a), several characteristic peaks were detected at 31.7°, 34.3°, 36.2°, 47.4°, 56.5°, 62.7°, 66.3°, 67.8°, 69°, and 76.8°, corresponding to the (100), (002), (101), (102), (110), (103), (200), (112), (201), and (202) miller indices that are assigned to hexagonal ZnO (a = 3.25, b = 3.25, and c = 5.21 Å), as indexed by (ICDD: 01-076-0704) standard data⁴⁷. The main characteristic diffraction peaks of g-C₃N₄ nanosheets and ZnO are observed for the ternary ZPG nanocomposite (Fig. 2a). Remarkably, the intensity of g-C₃N₄ nanosheets crystal faces and ZnO was reduced in the prepared ZPG due to the amorphous nature of PPy-NTS_, which suggests the fruitful development of the hybrid nanocomposite by implanting the PPy-NTs inside the prepared matrix⁴⁸.

Figure 2b depicts the FTIR spectra of the prepared samples. Concerning PPy-NTs, the bands at 1543 cm⁻¹ is attributed to C=C stretching mode of the pyrrole ring, respectively⁴⁹. N–H stretching vibration has been credited for the broad band at 3300 cm⁻¹, whereas the bands at 1310 cm⁻¹ and 1180 cm⁻¹, respectively, were accredited to anti-symmetrical C–N and C–H stretching^50,51. The Peaks at 1037 cm⁻¹ and 912 cm⁻¹ are connected to PPy’s doped state⁵⁰. The g-C₃N₄ exhibits a number of strong distinctive peaks attributed to the stretching vibrational modes of the heterocyclic rings between 1200 and 1700 cm⁻¹, as well as a peak at 808 cm⁻¹ attributed to the stretching vibrational modes of triazine units⁴⁰. The C₃N₃ stretching vibrational mode is attributed to the peak located at 1400 cm⁻¹. The O–H bending and stretching vibrational modes is also responsible for the peaks located at 1648 cm⁻¹⁵². According to ZnO, the typical characteristic peaks can be detected at, 845, 1190, 1382, and 1456 cm⁻¹⁵³. The broad peak at about 3200 cm⁻¹ is assigned to O–H stretching vibration of water⁵⁴. It is clear from that FTIR spectrum of the PGZ composite represented the mutual influence of PPy-NTs, g-C₃N₄, and ZnO by comparing with the corresponding distinctive peaks of PPy-NTs, g-C₃N₄, and ZnO. The peak strength and position, however, showed spectroscopic peak deviations, indicating interaction rather than a simple blending of the counterparts. Results from FT-IR confirm the development of PGZ nanocomposite that agrees well with results of the X-ray diffraction pattern.

The morphological characteristics of the as-prepared g-C₃N₄ nanosheets, PPy-NTs, ZnO NPs, and ZPG hybrid nanocomposite were investigated using FE-SEM. Figure 3a displays the SEM image of g-C₃N₄, revealing highly exfoliated graphene-like sheets. PPy-NTs exhibit a 1D uniform hollow nanotube-like structure (Fig. 3b). It is noteworthy that numerous nanotubes are wrapped around one another due to—interactions with the backbone chains of the PPy-NTs. From Fig. 3c, it can also be seen that the morphology of the ZnO nanoparticles displays -a spherical shape. Regarding ZPG nanocomposite at two different magnifications (Fig. 3d, e), intimate interaction between g-C₃N₄ nanosheets, PPy-NTs, and ZnO NPs can be detected, demonstrating the successful construction of hybrid nanocomposite.

Figure 3.

FE-SEM images of (a) g-C₃N₄ nanosheets, (b) PPy-NTs, (c) ZnO NPs, and (d, e) ZPG hybrid nanocomposite at different magnifications.

Additionally, the high-angle annular dark-field picture (HAADF) (Fig. 4a) and the corresponding elemental mapping analysis (EDX) (Fig. 4b–f) display the consistent distribution of C, N, Zn, and O along the hybrid composite surface. EDS analysis (Fig. 4g) also reveals that the g-C₃N₄ nanosheets, PPy-NTs, and ZnO NPs exist in the hybrid composite, which agrees with XRD results (Fig. 2a).

Figure 4.

HAADF image of ZPG hybrid nanocomposite (a), the resulting elemental mapping investigation (b–f) of C, N, Zn, and O, and EDS analysis of ZPG nanocomposite (g).

The anti-corrosion properties of the prepared nanocomposite coatings

EIS measurements were used to examine the corrosion effectiveness of nanocomposite coatings containing PPy-NTs, PPy-NTs/g-C₃N₄, and PPy-NTs/g-C₃N₄/ZnO nanocomposite. Figure 5 shows the Bode plots (Fig. 5a and b) and Nyquist plots (Fig. 5c) of epoxy resin-coated carbon steel without and with existence of the as-prepared materials after 168 h of immersion in 3.5% NaCl solutions. The case neat epoxy coating’s Nyquist plot reveals two loops⁵⁵. The neat epoxy coating film is the subject of the first high-frequency capacitance loop⁵⁶. The corrosion operations under the epoxy film are what cause the second loop, which occurs at low frequency⁵⁷. Figure 6 shows the equivalent circuit that was used for illustrating the above situation. The components of this equivalent circuit, which can be found in Table 1, include coating capacitance (C_c), the coating resistance (R_c), charge transfer resistance (R_ct), capacitance of the double layer (C_dl), and solution resistance (R_s). The values of chi-square values (χ²) in the Table 1 indicate goodness of fit. It is clear that the Nyquist spectrum alters when epoxy-coated carbon steel is combined with newly manufactured nano-materials. By adding as-prepared nano-materials, the sizes of both of the capacitive loops for coated carbon steel rises. This kind of system uses an equivalent circuit that is similar to the one employed for the neat epoxy coating (Fig. 6). The addition of as-prepared nanomaterials to epoxy resin coating considerably raised R_c, R_ct and lowered C_dl, C_c values, as shown in Table 1. The following is a list of the prepared nanocomposite coatings’ anti-corrosion effectiveness: EP/PPy-NTs/g-C₃N₄/ZnO ˃ EP/PPy-NTs/g-C₃N₄ ˃ EP/PPy-NTs. At 1.0 of PPy-NTs/g-C₃N₄/ZnO nanocomposite, the most effective epoxy coating effectiveness was attained. It is possible to argue that adding newly manufactured nano-materials to epoxy resin enhances the coating’s resistance to corrosion. This results from nano-particles lessening the epoxy resin's permeability, which slows the flow of corrosive ions to the surface of the metal⁵⁸.

Figure 5.

EIS spectra: (a) Bode-phase angle, (b) Bode-module, and (c) Nyquist plots of coated carbon steel covered with neat epoxy in the absence and presence of PPy-NTs, PPy-NTs/g-C₃N₄, and ZPG hybrid nanocomposite after 168 h immersion in 3.5% NaCl solutions at 298 K.

Figure 6.

Equivalent circuit model for coated carbon steel with the neat epoxy and nanocomposite coatings.

Table 1.

Impedance parameters for the carbon steel coated by epoxy composite coatings immersed in 3.5% NaCl solution at 298 K.

System	χ2	Rc kΩ cm2	Cc F cm−2	Rct kΩ cm2	Cdl F cm−2
Neat EP resin	0.00018	34.7	8.5 × 10–8	168.4	9.5 × 10–8
EP/PPy-NTs	0.00051	73.2	5.3 × 10–8	402.3	1.5 × 10–8
EP/PPy-NTs/g-C3N4	0.00034	94.4	1.9 × 10–8	512.7	1.5 × 10–9
EP/PPy-NTs/g-C3N4/ZnO	0.00038	123.6	0.5 × 10–8	632.5	0.4 × 10–9

The primary factor improving the corrosion protection of the EP/PPy-NTs/g-C₃N₄ coating is the mixing of PPy-NTs and g-C₃N₄. Where g-C₃N₄ nanosheets align each other parallel to the metal surface, reducing the route by which corrosive ions penetrate the surface of the metal and preventing corrosion^59,60. On another hand, the combination of g-C₃N₄ and ZnO provides better corrosion protection than g-C₃N₄ independently. This nano-composite (EP/PPy-NTs/g-C₃N₄/ZnO) has different levels of protection. Morsi et al.⁶¹ claim that nanoparticles made of ZnO can enhance their surface area by increasing the capacity of nanocomposites to be adsorbed on metal surfaces. They can also interact with the ions released from the corrosion condition, increasing the rate chance of occurrence. Furthermore, ZnO nanoparticles may enhance steel anticorrosion properties by catalysing oxygen reduction on the exterior of steel and increasing the nanocomposite's capacity to fill certain holes and flaws on the metal surface⁶². Meanwhile, ZnO attaches corrosive species like chloride. Furthermore, g-C₃N₄ occupies epoxy resin pores, reducing the overall amount of corrosive ions that penetrate the metal surface^63–66.

Polarization measurements were used to assess the anti-corrosion performance of nanocomposite coatings including PPy-NTs, PPy-NTs/g-C₃N₄, and PPy-NTs/g-C₃N₄/ZnO nanocomposite (see Fig. 7). The location of the intersection of Tafel plot points⁶⁷ was used to determine electrochemical kinetic variables (corrosion potential E_corr and corrosion current density j_corr). When neat EP resin was placed in 3.5% NaCl solution, j_corr was μA cm⁻². Carbon steel covered with PPy-NTs, PPy-NTs/g-C₃N₄, and PPy-NTs/g-C₃N₄/ZnO nanocomposites coatings, on the other hand, had significant reductions in j_corr values. j_corr was 7.3, 4.5, and 1.7 μA cm⁻² for PPy-NTs, PPy-NTs/g-C₃N₄, and PPy-NTs/g-C₃N₄/ZnO, respectively. Furthermore, the inclusion of PPy-NTs/g-C₃N₄/ZnO causes a positive change in the E_corr value from − 0.543 to − 0.401 V. This result reinforces up the EIS tests, which show that adding as-prepared nanoparticles to epoxy resin coating significantly improves its anti-corrosion capabilities.

Figure 7.

Polarization curves of coated carbon steel (dry-film thicknesses ≈ 33 µm) covered with neat epoxy in the absence and presence of PPy-NTs, PPy-NTs/g-C₃N₄, and ZPG hybrid nanocomposite in 3.5% NaCl solutions at 298 K.

Conclusions

Novel highly efficient anticorrosive ternary PPy-NTs/g-C₃N₄/ZnO nanocomposite (ZPG) nanocomposites were rationally fabricated via simple wet-impregnation technique. The performance of a novel epoxy coating (Epoxy/ZPG coating) on coated carbon steel in 3.5 wt% NaCl electrolyte was investigated. The outcomes demonstrated that ZPG in an epoxy coating exhibit superior anti-corrosion property to neat epoxy resin. This work may provide new insight into corrosion protection of epoxy coatings applications through the smart design of highly efficient materials.

Author contributions

All authors contribute in interpreting the experiments and writing the manuscript.

Data availability

The datasets used and/or analysed during the current study available from the corresponding author on reasonable request.

Competing interests

The authors declare no competing interests.