Inhibition effect of apium graveolens, punica granatum, and camellia sinensis extracts on plain carbon steel

Abstract

Application of plant extracts for corrosion inhibition of carbon steels continues to increase due to their nontoxic nature and presence of phytochemical components. The corrosion inhibition performance of Apium graveolens, Punica granatum, and Camellia sinensis plant extracts on plain carbon steel in 0.5 M sulfuric acid was assessed with coupon measurement, potentiodynamic polarization technique and optical microscopy characterization. The plant extracts effectively inhibited the carbon steel from 60% to 90% concentration with optimal inhibition efficiency values of 95.83%, 87.08%, and 92.37% at 90% concentration from coupon measurement. The corrosion inhibition capability of the plant extracts proves it to be time and concentration dependent, though time dependence decreases with increase in concentration and was negligible at 90% concentration. Polarization studies showed the extracts exhibited cathodic inhibition mechanism from the displacement of the polarization plots and significant decrease in cathodic portion of the polarization plots. Optical image of the steel without the extracts exhibited general corrosion with macro-pits which significantly differ from the image of the inhibited steel.

Keywords:

• plant extract
• corrosion
• green compounds
• steel
• inhibitor

PUBLIC INTEREST STATEMENTS

http://coventuniversity.edu.ng The economic impact and problems resulting from corrosion has drawn strong attention from scientists and engineers worldwide. Corrosion of mild steel in industrial environments is a major concern in chemical processing plants, oil and gas industry, manufacturing, automobile industry, marine operations, boiler plants, and power generation plants due to the considerable cost involved in the replacement of metallic parts in their various applications. The consequence often leads to plant shutdowns, breakdown of industrial equipment, reduced efficiency, industrial downtime, high maintenance cost due to replacement of damaged part, wastage of valuable resources, and expensive overdesign. Corrosion inhibition by environmentally sustainable biodegradable compounds is of great practical importance compared to conventional toxic chemical compounds due to the long-term benefits to the environmental and personnel safety.

1. Introduction

Corrosion is the degradation of the metallurgical, physical, microstructural, and mechanical properties of metallic alloys due to chemical reaction processes between the alloys and their surrounding (Gilbert, 2012; Rajendrachari, 2018). It is an inherent, spontaneous and thermodynamic process whereby the materials return to their more chemically stable forms, i.e. corrosion products such as oxides, hydroxides, sulfides, etc. at lower energy state (Mokhatab et al., 2019). The corrosion products is due to the ionization of the metallic ions which diffuses into the corrosive environment and probably undergoes secondary reaction; chemically combining with other ions present to form an insoluble molecular species such as rust (Alcántara et al., 2017). This phenomenon is common in industrial processes such as refinery operations in crude distillation units, production of intermediate chemical compounds, fertilizer production, pickling operations, etc. where acidic solutions are extensively applied thus increasing the vulnerability of metallic components within this conditions to corrosion (Fiori-Bimbi et al., 2015). The effect of corrosion on domestic economies worldwide reaches about 3.1% of national GDP (Gilbert, 2012). According to Shreir (2010), destruction of refined materials due to corrosion is ranked third after conflict and epidemic. Corrosion effect on metals is more conspicuous and deleterious compared to nonmetallic materials resulting in metallic wastage due to the action of corrosive agents. Mild steel is a ferrous alloy composed of 0.1–0.25% C content with versatile application in civil and industrial construction (Kilcherman, 2015). Petrochemical pipelines, some automobile parts, marine structures, and industrial machinery are constructed with mild steel. The steel is relatively inexpensive compared to stainless steels. It is weldable and recyclable coupled with high machinability (Lgaz et al., 2018). Electrochemical deterioration of mild steel occurs readily in electrolyte solution during pickling and scale-removal, transportation of acids, boiler operations, heat transfer in nuclear reactions, and other industrial processes. Its poor corrosion resistance results in accelerated general corrosion propagated throughout the entire exposed surface. General corrosion is the most destructive cause of mild steels degradation on tonnage basis, as a result the steel requires continual maintenance, repairs, and replacement leading to huge overhead and operating costs (Aminu, 2015). There are a number of corrosion control methods such as materials selection, changes in design philosophies and the adoption of varied prevention techniques, which are in common use. Usage of chemical derivatives known as corrosion inhibitors is an economic means of corrosion mitigation and control. These chemical compounds alter the reduction-oxidation reaction mechanism through modification of the corrosive media and alteration of the electrochemical reaction between the steel and the corrosive media (Amitha & Basu, 2012). Most corrosion inhibitors being of organic and inorganic origin are highly effective but toxic to the environment (Marko & Chigondo, 2016; Sığırcık et al., 2016). Previous research has shown plant extracts to be promising compounds that suppresses metal-electrolyte reactions (El-Etre, 1998, 2003, 2006; Ebenso et al., 2004; Ebenso & Ekpe, 1996; Ibrahim et al., 2012; Li, Deng,  et al., 2012; Li , Deng, Fu, et al., 2014; Li, Deng, Xie, et al., 2014; Li, Zhang et al., 2012; C.A. Loto et al., 2011; Loto & Olowoyo, 2018; R.T. Loto et al., 2018; Loto, 2018; Mourya et al., 2014). The need for nontoxic and cost-effective compounds emphasizes the importance of environmental protection, sustainability and human health concerns. The wide spread availability of plant extracts makes them appropriate alternatives in contrast to the costly and harmful convention organic and inorganic corrosion inhibitors. Plant extracts are biodegradable, ecologically acceptable, cost effective, and renewable. In contribution to the research on application of plants extracts for corrosion prevention and control, this article evaluates the corrosion prevention properties of Apium graveolens, Punica granatum, and Camellia sinensis plant extracts on plain carbon steel in 0.5 M H₂SO₄ solution. The major chemical compositions of the extracts are shown in Figure 1.

Figure 1. Major chemical compositions of (a) apium graveolens, (b) punica granatum, and (c) Camellia Sinensis.

2. Experimental methods

2.1. Materials and preparation

Plain carbon steel (PCS) rod (6 mm length and 12 mm diameter) has nominal content (wt. %) of 0.05% S, 0.04% P, 0.8% Mn, 0.16% C, and 98.95% Fe. The steel rod was cut and machined into 21 samples, and subsequently washed with deionized H₂O and CH₃COCH₃. Apium graveolens (APG), Punica granatum (PCG), and Camellia sinensis (CLS) were purchased from Shoprite, Lagos, Nigeria. 1.2 Kg of APG and PCG were separately cut to very small pieces together with the bark and blended. The grinded solutions were sifted to get the fluid concentrate. CLS was extricated utilizing a rotational evaporator in 3 L of deionized H₂O. APG, PCG, and CLS were separately prepared in volumetric concentrations of 10%, 15%, 30%, 45%, 60%, 75%, and 90% per 200 mL of 0.5 M H₂SO₄ solution.

2.2. Coupon measurement

PCS samples were independently deposited in 200 mL of 0.5 M H₂SO₄ solution and weighed at 24 h interval for 240 h. Corrosion rate, Ĉ (mm/y) was obtained from the following equation;

(1) $\hat{c}=\left[\frac{87.6\omega }{DAt}\right]$(1)

ω represents weight loss (g), D represents density (g/cm³), A represents visible surface area of PCS specimen (cm²), 87.6 represents corrosion rate constant, and t represents duration of the experiment (h). Inhibition efficiency η (%) was obtained from the formula below;

(2) $\eta =\left[\frac{{\omega }_1-{\omega }_2}{{\omega }_1}\right]\times 100$(2)

ω₁ and ω₂ represents weight loss of PCS at predetermined APG, PCG, and CLS concentrations. Inhibitor coverage of the steel was obtained as follows:

(3) $\theta =\left[1-\frac{{\omega }_2}{{\omega }_1}\right]$(3)

where θ represents inhibitor coverage on PCS.

2.3. Potentiodynamic polarization

Electrochemical evaluation of PCS was performed at 30^◦C surrounding temperature. A triple electrochemical cell consisting of platinum counter electrical conductor, silver chloride reference electrical conductor containing 3 M KCl solution at pH of 6.5 and PCS working electrical conductor were submerged inside a specialized cell filled 200 mL of H₂SO₄/plant extract (APG, PCG and CLS) solution. The electrode configuration was interfaced with potentiostatic device (Digi-Ivy 2311) and computer. PCS working electrode was encased in hardened Versocit metallographic mounts with visible surface dimension of 1.13 cm². Polarization curves were produced at scan rate of 0.0015 V/s from −0.75 V to +1.5 V. Corrosion current density C_J (A/cm²) and corrosion potential C_P (V) values were gotten from Tafel extrapolation. Corrosion current C_I (A) was obtained from the intercept between the anodic-cathodic portions of the polarization curves. Corrosion rate, Ĉ (mm/y) was calculated as follows;

(4) $\hat{c}=\frac{0.00327\times J_{\mathrm{c}\mathrm{r}}\times E_{\mathrm{v}}}{D}$(4)

E_v represents PCS equivalent weight (g), 0.00327 represents constant for corrosion calculation, and D represents the density (g/cm³).

2.4. Optical macroscopy analysis

Optical macrographs of degraded PCS surface from noninhibited electrolyte was analyzed and matched with APG, PCG, and CLS inhibited PCS surface after corrosion tests using Omax trinocular metallurgical microscope.

3. Results and discussion

3.1. Coupon measurement

Figure 2(a) - 4(b) shows the plots of PCS corrosion rate and plant extracts (APG, PCG, and CLS) inhibition efficiency against exposure time. Table 1 shows the data for weight loss, corrosion rate and inhibition efficiency from coupon measurement at 240 h. Results for corrosion rate of PCS at 0% APG, PCG and CLS concentrations contrast the values at 45%, 60%, 75%, and 90% inhibitor concentration due to the degradation effect of SO₄^2- anions on ionized PCS surface in the acid solution. PCS corrosion rate values at 24 h (137.92 mm/y, 113.22 mm/y and 138.47 mm/y) decreased to 45.49 mm/y, 45.51 mm/y, and 46.3 mm/y at 240 h. The SO₄^2- anion caused the oxidation of PCS surface and release of Fe²⁺ anions into the solution, effectively degrading the entire steel surface throughout the exposure period. Addition of APG, PCG and CLS inhibitor compounds at 15% and 30% concentration caused significant decrease in corrosion rate to values between 71.66 mm/y and 53.09 mm/y at 24 h. However, the overall effect of the inhibitor compounds (15% and 30% concentrations) at 240 h is negligible with PCS corrosion rate values not differing from its value at 0% inhibitor concentration. At 15% and 30% concentration, the molecules of the inhibitor compounds were insufficient to counteract the degradation effect of the corrosive anions and possibly modify the corrosive medium through the formation of complexes less harmful to the steel surfaces. At 45% inhibitor concentration, the inhibition performance of APG, PCG, and CLS where under 40% while at 60% concentration only the inhibition performance of APG compound crossed the 50% barrier to 54.55%. The performance of APG, PCG and CLS compounds significantly improved at 75% concentration to values of 85.74%, 82.85%, and 62.7%. These observations show the inhibition performance of APG, PCG, and CLS compounds are significantly concentration dependent, though changes in the plots configuration (Figure 2(a)-4(b)) confirm time dependence of the inhibitor. However, the inhibition performance of the inhibitors gradually reduces with rise in inhibitor concentration and time. At 90% inhibitor concentration, the performance index of APG, PCG, and CLS (95.83%, 87.08%, and 92.37%) at 240 h of exposure results from plot configurations whose time dependence is negligible. At 75% concentration, APG and CPG inhibitor were time dependent to a small degree while CLS inhibitor still showed relatively significant time dependence. Results exhibited from the performance of the plant extracts in the acid electrolyte show effective inhibition performance begins at 60%.

Figure 2. Plot of (a) PCS corrosion rate and (b) APG inhibition efficiency versus exposure.

Figure 3. Plot of (a) PCS corrosion rate and (b) CPG inhibition efficiency versus exposure.

Figure 4. Plot of (a) PCS corrosion rate and (b) CLS inhibition efficiency versus exposure.

Table 1. Data of PCS weight loss and corrosion rate, and APG, PCG, and CLS inhibition efficiency at 240 h

Samples	Inhibitor Conc. (%)	APG			PCG			CLS
		Weight Loss (g)	Ĉ (mm/y)	η (%)	Weight Loss (g)	Ĉ (mm/y)	η (%)	Weight Loss (g)	Ĉ (mm/y)	η (%)
A	0	5.570	45.49	0	5.127	45.51	0	5.263	46.72	0
B	15	5.324	47.26	4.49	3.980	35.33	22.37	5.249	46.59	0.26
C	30	5.053	44.86	9.35	5.030	34.65	31.89	5.216	46.30	0.89
D	45	4.188	37.18	24.87	3.386	30.05	33.96	4.685	41.59	10.97
E	60	2.534	22.49	54.55	2.633	23.37	48.65	3.558	31.58	32.39
F	75	0.795	7.06	85.74	0.879	7.81	82.85	1.963	17.43	62.70
G	90	0.233	2.06	95.83	0.663	5.88	87.08	0.401	3.56	92.37

3.2. Optical microscopy analysis

Optical representations of PCS surface prior to corrosion test, and after corrosion in 0.5 M H₂SO₄ solution with and without the addition of plant extracts are displayed from Figure 5(a) to Figure 7 at mag. ×25. Figure 5(a) exhibits the morphology of PCS before corrosion. The serrated morphology is due to machining of the steel surface. The morphology in Figure 5(b) is due to the oxidation effect of SO₄^2- anion reactions, which is the causative factor for the degradation of the steel surface. The corroded morphology results from general corrosion in addition to the growth of macro-pits. The oxidation of the steel surface caused the release of iron (II) oxide into the acid solution. Figures 6(a-b) and 7 displays the morphology of PCS after corrosion test in the presence of APG, CPG, and CLS inhibitor. The improved morphologies are due to the inhibiting action of the plant extracts. The mild surface deterioration is due to the gradual inhibitive action of the plant extracts. Further analysis from potentiodynamic polarization, which will be discussed later showed the plant extracts displayed dominant cathodic inhibition. Hence the inhibition mode of the plant extracts results from the modification of the corrosive media, whereby the molecules of the plant extracts reacts with the anions of the corrosive solution, hence limiting the cathodic reaction mechanism.

Figure 5. Surface morphology of (a) PCS before corrosion and (b) PCS after corrosion in 0.5 M H₂SO₄ solution.

Figure 6. Surface morphology of (a) PCS after corrosion in 0.5 M H₂SO₄/APG solution and (b) PCS after corrosion in 0.5 M H₂SO₄/CPG solution.

Figure 7. Surface morphology of PCS after corrosion in 0.5 M H₂SO₄/CLS solution.

3.3. Potentiodynamic polarization studies

Potentiodynamic polarization curves displaying the inhibition effect of APG, PCG, and CLS on PCS corrosion in 0.5 M H₂SO₄ solution are shown from Figures 8-10. Tables 2–4 show the polarization data for PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% APG, PCG, and CLS concentration. The trend in corrosion rate results and inhibition efficiency are generally similar to the data observed from coupon measurement. The anodic cathodic polarization plots for APG inhibition performance on PCS corrosion indicates mixed inhibition effect with respect to the shift in corrosion potential values in Table 2. The maximum variation in corrosion potential of the control sample is less than 85 mV. Hence APG molecules influenced the oxidation reaction mechanism on the steel surface where loss of valence electrons leading to the formation of Fe²⁺ is suppressed. H₂ evolution and consequentially O₂ reduction cathodic reactions are simultaneously hindered. Observation of the polarization plot in Figure 8 confirms this assertion; the presence of APG inhibitor (15%–45% concentration) decreased the anodic-cathodic polarization plots of PCS corrosion. However, the change has negligible influence on the inhibition of PCS corrosion considering the inhibition efficiency values obtained (15.05%, 28.66%, and 37.93%). Further increase in APG concentration (from 60% to 90%) decreased the slopes further with improved inhibition efficiency values of 60.24%, 90.03%, and 96.70%. At 90% APG concentration the cathodic slope of PCS is more significantly influence indicating dominant cathodic inhibition despite its mixed inhibition property.

Table 2. Potentiodynamic polarization data of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% APG concentration

Sample	APG Conc. (%)	PCS Ĉ (mm/y)	APG η (%)	CI (A)	CJ (A/cm^2)	CP (V)	Rp (Ω)	Bc (V/dec)	Ba (V/dec)
A	0	20.69	0	2.05E-03	1.81E-03	−0.476	24.50	−9.384	0.000
B	15	17.58	15.05	1.74E-03	1.54E-03	−0.464	59.21	−8.102	20.500
C	30	14.76	28.66	1.46E-03	1.29E-03	−0.488	112.70	−6.999	12.790
D	45	12.84	37.93	1.27E-03	1.13E-03	−0.463	149.21	−8.971	16.950
E	60	8.23	60.24	8.15E-04	7.21E-04	−0.478	237.03	−8.068	13.360
F	75	2.06	90.03	2.04E-04	1.81E-04	−0.477	354.25	−8.294	12.500
G	90	0.68	96.70	6.75E-05	5.97E-05	−0.506	380.50	−9.608	15.440

Table 3. Potentiodynamic polarization plots of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% PCG concentration

Sample	PCG Conc. (%)	PCS Ĉ (mm/y)	PCG η (%)	CI (A)	CJ (A/cm^2)	CP (V)	Rp (Ω)	Bc (V/dec)	Ba (V/dec)
A	0	20.69	0	2.05E-03	1.81E-03	−0.476	24.50	−9.384	4.013
B	15	14.64	29.22	1.45E-03	1.28E-03	−0.994	56.30	−8.444	18.360
C	30	13.26	35.90	1.31E-03	1.16E-03	−0.976	66.50	−8.596	17.530
D	45	12.22	40.96	1.21E-03	1.07E-03	−0.986	76.30	−8.472	18.330
E	60	10.22	50.62	1.01E-03	8.95E-04	−0.988	94.30	−0.488	15.050
F	75	1.82	91.19	1.81E-04	1.60E-04	−0.980	194.53	−8.081	15.870
G	90	1.29	93.75	1.28E-04	1.13E-04	−1.044	200.60	−8.973	13.200

Table 4. Potentiodynamic polarization plots of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% CLS concentration

Sample	CLS Conc. (%)	PCS Ĉ (mm/y)	CLS η (%)	CI (A)	CJ (A/cm^2)	CP (V)	Rp (Ω)	Bc (V/dec)	Ba (V/dec)
A	0	20.69	0	2.05E-03	1.81E-03	−0.476	24.50	−9.384	4.013
B	15	20.32	1.79	2.01E-03	1.78E-03	−0.487	24.64	−8.057	2.056
C	30	20.12	2.77	1.99E-03	1.76E-03	−0.476	25.57	−7.596	5.510
D	45	15.65	24.37	1.55E-03	1.37E-03	−0.983	31.43	−8.342	3.544
E	60	12.93	37.49	1.28E-03	1.13E-03	−0.982	48.36	−8.206	15.000
F	75	5.10	75.37	5.05E-04	4.47E-04	−0.984	83.62	−8.030	14.930
G	90	2.67	87.10	2.64E-04	2.34E-04	−0.987	97.22	−8.116	16.310

PCG and CLS exhibited significant cathodic inhibition effect at most concentrations from observation of the polarization curves depicted in Figures 9 and 10. The polarization plots in Figure 9 shifted significantly from −0.476 V at 0% PCG to values between −0.994 V and −1.044 V. The potential difference is significantly above 85 mV signifying it belongs to the cathodic class of corrosion inhibitors. PCG decreased the cathodic and anodic polarization plots of PCS corrosion after 15% concentration. At 90% concentration, the cathodic polarization plot decreased further due to cessation of the H₂ evolution and O₂ reduction reactions on PCS surface. The inhibition efficiency results of PCG attained effective values from 60% concentration similar to the observation for APG inhibitor. The performance of CLS inhibitor was significantly poor at 15% and 30% concentration relative to APG and CPG inhibitor. Between 45% and 60% concentration, relative improvement in inhibition efficiency occurred but the value is below effective inhibition performance until 75% and 90% inhibition efficiency where the values are 75.37% and 87.10% respectively.

Figure 8. Potentiodynamic polarization plots of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% APG concentration.

Figure 9. Potentiodynamic polarization plots of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% PCG concentration.

Figure 10. Potentiodynamic polarization plots of PCS corrosion in 0.5 M H₂SO₄ solution at 0%−90% CLS concentration.

4. Conclusion

Apium graveolens, Punica granatum, and Camellia sinensis plant extracts effectively inhibited the corrosion of plain carbon steel in dilute acid solution at high concentrations. The performance of the extracts was significantly concentration dependent and to a lesser extent time dependent. The extracts exhibited cathodic inhibition effect suppressing the H₂ evolution and O₂ reduction reactions. In the absence of plant extracts, plain carbon steel underwent general surface degradation coupled with significant macro-pits. The steel morphology significantly improved in the presence of the plant extracts in the corrosive media.

Acknowledgments

The author acknowledges the support of Covenant University, Ota, Nigeria for the provision of research facilities for this work and the laboratory contribution of Fope Oyedeko.

Disclosure statement

Authors declare no conflict of interest.

Additional information

Funding

The authors received no direct funding for this research.

Notes on contributors

Roland Tolulope Loto

Prof. Roland Tolulope Loto is a lecturer and researcher at Covenant University. He is proven scholar in the field of metallic corrosion prevention and control. He has over one hundred and eighty (180) research publications. He has consistently served as reviewer in respectable journals due to his intensive knowledge and technical expertise. Roland has undertaking a number renowned engineering research in collaboration with research/educational institutions. His in-depth experience in research experimentation basically aimed at proffering solutions to the current depreciating effect of metallic degradation and failure in service in various engineering and industrial applications. He has a Doctor of Technology (DTech) in Metallurgical and Materials Engineering (2014) from Tshwane University of Technology, Pretoria, South Africa, Master’s Degree (MSc) in Metallurgical and Materials Engineering (2007) from University of Lagos, Lagos, Nigeria and a Bachelor of Technology in Mechanical Engineering (2002) from Ladoke Akintola University of Technology, Oyo State, Nigeria.