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Correlative evaluation of the corrosion resilience and passivation properties of zinc and aluminum alloys in neutral chloride and acid-chloride solutions

  • Roland T. Loto EMAIL logo
Published/Copyright: January 24, 2024
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Abstract

Comparative analysis of the corrosion resilience and passivation characteristics of pure zinc (Zn) and aluminum (Al) alloys in neutral chloride and acid-chloride solutions at 0.5–3% NaCl concentrations was done with potentiodynamic polarization, potentiostatic evaluation, optical characterization, and open circuit potential measurement. Results show Al alloy was more resistant to general corrosion in both solutions with values ranging from 0.031 to 0.082 mm/year, and 0.037 to 0.389 mm/year compared to Zn alloys with values of 0.432–0.691 mm/year and 0.465–5.016 mm/year. Corrosion potential values of Zn alloy were significantly more electronegative than the values for Al alloy. The passivated region of the polarization plots for Al was thermodynamically unstable with visible current transients compared to that of Zn. Passivation of Al occurred at the early onset of anodic polarization in the neutral chloride solution. Zn alloy passivated at specific potentials, coupled with stable passivation behavior. The passivation range values of Al were generally greater than the values for Zn due to delayed stable pitting activity. Optical images for Al showed extensive localized degradation along specific regions and grain boundaries, whereas Zn morphology indicates general surface degradation. Open circuit potential plots indicate significant growth of Al2O3 oxide on Al coupled with active–passive transition behavior of the oxide. This contrasts the observation for Zn where the plot configuration indicates limited oxide formation and growth but significant thermodynamic stability.

1 Introduction

Fe-based alloys have extensive industrial applications worldwide due to their versatility, relative ease of production, availability, and exceptional mechanical properties for applications that require structural rigidity, stiffness, and extended lifespan [1,2,3,4,5,6]. One of the major limitations in the application of Fe-based alloys is their vulnerability to corrosion, though this is more associated with the carbon-based ferrous alloys whose failure in corrosive environments results in economic and financial loss. Stainless steels with sufficient Cr, Ni, Ti, Mb, etc., content are significantly more resistant to corrosion, but their advantages are offset by their relatively high cost of production and utilization [7,8,9]. This necessitates the need for low-cost alternatives with respect to corrosion protection of metallic parts, structures, columns, fittings, pipes and components, and mechanical properties. However, other important factors that must be taken into consideration are the cost of production, lower cost of application, etc. [10,11,12,13]. The application of Zn coatings has been proven to be one of the most resilient and proven methods of protection of ferrous alloys. This is possible by cold-dip galvanizing, hot-dip galvanizing, galvannealing, electro-galvanizing, continuous-line galvanizing, zinc plating and spraying, mechanical plating, and zinc-pigment paints [14]. Being the fourth most applicable metal worldwide and twenty-third most represented element within the earth’s crust (0.013%), about 50% of Zn produced is used in the Zn galvanizing technique [15,16,17]. The other significant industrial utilization of Zn includes white discoloration in paints, stimulant in rubber processing, manufacture of precautionary agents for rubber polymers and plastics, production of photocopying parts [18,19], catalyst in prototype rockets [20], protective coating for cover sheets, and oil and gas infrastructure [21,22]. Al alloy is extensively utilized in the production of industrial components, civil engineering applications, telecommunication wires, boilers, degradation-resistant containers, chemical production, and welding of aluminum parts [23]. Al metal makes up about 8% of the elemental composition of the Earth’s crust. Its economic importance is second to Fe. The strength and density to mass proportion, electrical and heat conduction, low- and high-temperature stability, non-toxicity, mechanical properties, corrosion resistance, and industrial relevance [24,25]. The aluminum industry yields $174 billion to the American Gross Domestic Product and about $70 billion yearly in direct economic output [26]. Al alloys are significantly applied in the manufacture of parts for vehicles, chemical production plants, energy-generating plants, aeroplanes, infrastructures, etc. [27,28,29,30]. The properties of Al can be modified to align distinct industrial and engineering requirements.

The corrosion resistance of Zn is due to the growth of a passive inert oxide film which hinders further corrosion reaction mechanisms when exposed to the atmosphere. The passive inert oxide film occurs due to the reaction of Zn with O2 resulting in the evolution of Zn(OH)2 and thereafter ZnCO3 after reacting with CO2 [31]. The electrochemical property of Zn to sustain a protective oxide is mainly determined by the pH of the environment, especially acidic pollutants. Because zinc forms an amphoteric oxide, strong alkalinity can also adversely affect zinc’s corrosion behavior by interfering with the formation of protective layers [32]. Salt composition within marine conditions also significantly influences Zn corrosion [33]. Al displays significant resistance to corrosion degradation because of the formation of Al2O3 on its surface [34]. Howbeit, its structural strength and functional lifespan can be severely reduced in corrosive environments containing minimal concentrations of Cl, SO4 2−, etc. The protective oxide deteriorates in the presence of threshold concentrations of the corrosive anions [35,36]. A number of theories are available on the mechanism of deterioration of the inert oxide on metallic alloys resulting from the electrolytic transport of reactive species through the protective oxide to the metal. Previous studies show that reactive species interact with the protective oxide leading to its deterioration through the evolution of metallic complexes [37,38]. Other studies suggest deterioration in Cl anion electrolyte is related to the intermetallic phase and elemental composition which limits their economic relevance [39]. It has been proven that the protective oxide on metallic alloys is normally stable at minimal anionic concentrations [40,41,42]. A study on the effect of corrosive anions on Al-based galvanic anodes indicates pitting potential decreased with an increase in anionic content whereas other anionic species showed a passivating effect [43]. Effective utilization of Zn and Al alloys results from adequate information on the corrosive nature of the applicable environments, degradation rate, and type of corrosion. Localized corrosion of Zn and Al can be ascertained by their characteristics, size, microstructural properties, and electrochemical properties at the metal-solution interface This necessitates appropriate comprehension of the nature and process of interaction of the corrosive anions with the metal exterior in aqueous solutions. A number of corrosion resistance studies have been performed on Zn and Al.

Graedel studied the corrosion of Zn in the atmosphere. Observation shows that the corrosion layer formation and the chemical reactions involved are a direct consequence of the pH of the aqueous surface film due to its influence on the dissolution of the passive oxyhydroxide surface [44]. Ferry and Mohd Sukarnoor studied the corrosion reaction processes of Zn-coated mild steel in saline aqueous media. Results showed the degradation rate of fully coated steel reduces with exposure time while the values for the Zn coated with scratch were slightly higher [45]. The atmospheric behavior of hot-dip Zn galvanized and Al-coated steel wire strands from long-term exposure tests in rural sulfur, industrial, and marine areas of the islands of Taiwan was studied by Yaw-Tzong et al. The major corrosion product for the Zn-coated steel in severe marine environments was found to be Fe2O3, and no zinc coating was left for the protection of the base steel after 2 years [46]. Al-Moubaraki and Al-Rushud studied the corrosion behavior of Al 7075, Al 2024, and Al 6061 in the Red Sea water. Results obtained showed that the corrosion rates exhibit a continuous decrease with exposure time. The order of corrosivity of the Al alloys is Al 6061 < Al 2024 < Al 7075. Pitting corrosion was the prevalent corrosion pattern detected on alloys [47]. According to Seyeuxa et al. [48], degree of localized corrosion damage differs with regard to the concentration of corrosive species and the type of aqueous environment. There is a need to further evaluate the inert film on metallic alloys to comprehend the mechanism associated with the collapse and reformation of the protective oxides which is the focus of this investigation. Silva et al. [49] and Mollapour and Poursaeidi [50] studied the deterioration of the passive film on stainless steel and established that the strength of the inert oxide to electrochemical degradation is substantially controlled by external factors. In agreement with Pao et al. [51], Zhang et al. [52], Liu et al. [53], and Calderon et al. [54] showed that resistance to pit formation and growth with steel results from different determinant variables associated with industrial environments and metallurgical properties of the alloy. On account of citation [49,50,51,52,53,54], this research studies the localized corrosion resistance, passivation properties, and polarization behavior of Zn and Al alloys in neutral chloride and acid-chloride solutions.

2 Materials and methods

2.1 Materials and preparation

Flat squared zinc (Zn) sheets with surface proportions of 100 mm by 100 mm by 50 mm (length, breadth, and thickness) and cylindrical aluminum alloy (Al) were cut into six work samples with a median configuration of 1 cm by 1 cm (length and breadth) using manual hand tool for potentiodynamic polarization, optical microscopy, and open circuit potential evaluation. Elemental analysis of the Al and Zn work samples were analyzed with PhenomWorld high-resolution electron microscope. The wt% compositions of Al and Zn are shown in Table 1. Cu cables were affixed to Al and Zn work samples with soft solder before being enmeshed with pre-solidified acrylic paste. The exterior area of the Al and Zn work samples was graded with SiC sheets (60–1,500 grits), brightened with a 3 µm diamond mixture, and washed with de-mineralized H2O and dimethyl ketone. Neutral chloride solution prepared from recrystallized NaCl (obtained from Titan Biotech, India) at 0.5, 1, 1.5, 2, 2.5, and 3% NaCl concentration. Acid-chloride solution (0.0015 M H2SO4 containing 0.5, 1, 1.5, 2, 2.5, and 3% NaCl concentration) was prepared from standard class H2SO4 acid solution obtained from Sigma-Aldrich, USA.

Table 1

Wt.% Composition of Al and Zn alloys

Element Fe Si Cu Zn Ti Mg Pb Sn Al
Al alloy
Wt% composition 0.232 0.078 0.0006 0.0016 0.006 0.0027 0.0012 0.007 99.66
Element Fe Si Cu Zn Ti Mg Pb Sn Al
Zn alloy
Wt% composition 100

2.2 Potentiodynamic polarization and open circuit potential evaluation

Corrosion kinetics was evaluated with potentiodynamic polarization while corrosion thermodynamics was determined by open circuit potential evaluation. Both tests were done at 308 K (ambient temperature) by adopting a Digi-Ivy 2311 potentiostatic apparatus. The apparatus which consists of a triple cord electrode (Al and Zn work sample electrode, Ag/AgCl threshold electrode, and Pt cord counter electrode) was networked to a laptop computer. Polarization data lines were produced at plot progression of 0.0015 V/s initiating at −2 to +0.75 V. Corrosion potential, C p (V), and corrosion current density C j (A/cm2) results were acquired by Tafel computation. Corrosion rate C r (mm/year) was retrieved from the numerical values below;

(1) C RT = 0.00327 × C J × C q D .

Here, E w indicates the equivalent weight (g) of Al and Zn, 0.00327 represents corrosion constant while D is the density (g/cm3). Polarization resistance P rt, (Ω) was assessed from the following numerical formula:

(2) P rt = 2.303 B a B c B a + B c 1 I cr ,

where B a and B c indicate anodic and cathodic Tafel curves (V/dec).

2.3 Optical microscopy analysis

Optical illustrations of Al and Zn work samples prior to and following potentiostatic analysis in neutral chloride and acid-chloride media at specific NaCl concentrations were obtained and studied with an Omax trinocular metallurgical microscope.

3 Results and discussion

3.1 Potentiodynamic polarization studies

The potentiodynamic polarization plots for Al and Zn alloy corrosion in neutral chloride and chloride sulfate electrolytes are shown in the following figures. Figure 1(a) and (b) demonstrates the corrosion polarization plots for Al and Zn alloys in neutral chloride media (0.5–3% NaCl concentration) while Figure 2(a) and (b) illustrates the corrosion polarization plots for Al and Zn alloys in 0.0015 M H2SO4 media at 0.5–3% NaCl concentration in 0.0015 M H2SO4 solution. Tables 2 and 3 presents the polarization data obtained for both alloys from the neutral chloride and acid-chloride solutions. The cathodic part of the polarization curves in Figure 1(a) and (b) substantially varies from each other. The plots in Figure 1(a) depict a similar slope configuration after 0.5% NaCl concentration which indicates the cathodic-reduction reaction of the redox reaction process (H2 evolution and O2 reduction) occurs under the activation mechanism. The cathodic slope configuration for Zn shows a limited Cl anion concentration effect on the cathodic reaction process which invariably alters the corrosion potential of the alloy [55]. Generally, the cathodic reaction occurs according to equations (3)–(5) as follows:

(3) 2 H + + 2 e H 2 ,

(4) O 2 + 2H 2 O + 4e 4OH ,

(5) O 2 + 4H + + 4e 2H 2 O .

Figure 1 
                  Potentiodynamic polarization diagram of (a) Al alloy and (b) Zn alloy in neutral chloride media (0.5–3% NaCl concentration).
Figure 1

Potentiodynamic polarization diagram of (a) Al alloy and (b) Zn alloy in neutral chloride media (0.5–3% NaCl concentration).

Figure 2 
                  Potentiodynamic polarization diagram of (a) Al alloy and (b) Zn alloy in 0.0015 M H2SO4 media at 0.5–3% NaCl concentration.
Figure 2

Potentiodynamic polarization diagram of (a) Al alloy and (b) Zn alloy in 0.0015 M H2SO4 media at 0.5–3% NaCl concentration.

Table 2

Potentiodynamic polarization values for Al and Zn corrosion in neutral chloride media (0.5–3% NaCl concentration)

NaCl conc. (%) Corrosion rate (mm/year) Corrosion current (A) Corrosion current density (A/cm2) Corrosion potential (V) Polarization resistance, R p (Ω) Cathodic Tafel slope, B c (V/dec) Anodic Tafel slope, B a (V/dec)
Al alloy
0 0.031 2.79 × 10−6 2.79 × 10−6 −1.019 9201.00 −7.843 4.240
0.5 0.043 3.95 × 10−6 3.95 × 10−6 −0.925 6504.00 −13.710 3.019
1 0.062 5.65 × 10−6 5.65 × 10−6 −0.848 4725.00 1.446 −1.413
1.5 0.085 7.74 × 10−6 7.74 × 10−6 −0.915 3318.00 −7.894 2.963
2 0.084 7.59 × 10−6 7.59 × 10−6 −0.930 3408.00 −7.164 13.720
2.5 0.086 7.84 × 10−6 7.84 × 10−6 −0.867 3015.00 −19.830 1.601
3 0.082 7.48 × 10−6 7.48 × 10−6 −0.814 3814.00 −10.550 4.137
Zn alloy
0 0.432 2.90 × 10−5 2.90 × 10−5 −1.230 886.30 −2.567 −2.737
0.5 0.453 3.04 × 10−5 3.04 × 10−5 −1.233 823.20 −2.926 −2.119
1 0.465 3.12 × 10−5 3.12 × 10−5 −1.292 796.10 −6.559 2.278
1.5 0.481 3.23 × 10−5 3.23 × 10−5 −1.301 723.70 −6.422 2.943
2 0.554 3.72 × 10−5 3.72 × 10−5 −1.240 691.40 −2.212 0.046
2.5 0.653 4.38 × 10−5 4.38 × 10−5 −1.251 653.20 −2.420 −3.202
3 0.691 4.63 × 10−5 4.63 × 10−5 −1.250 586.70 −3.037 −2.941
Table 3

Potentiodynamic polarization values for Al and Zn corrosion in 0.0015 M H2SO4 media at 0.5–3% NaCl concentration

NaCl conc. (%) Corrosion rate (mm/year) Corrosion current (A) Corrosion current density (A/cm2) Corrosion potential (V) Polarization resistance, R p (Ω) Cathodic Tafel slope, B c (V/dec) Anodic Tafel slope, B a (V/dec)
Al alloy
0.5 0.037 3.34 × 10−6 3.34 × 10−6 −0.857 5811.00 8.056 14.910
1 0.049 4.42 × 10−6 4.42 × 10−6 −0.801 7694.00 −1.535 21.120
1.5 0.386 3.51 × 10−5 3.51 × 10−5 −0.698 733.10 −0.614 14.400
2 0.384 3.49 × 10−5 3.49 × 10−5 −0.698 748.40 −3.414 12.080
2.5 0.385 3.50 × 10−5 3.50 × 10−5 −0.701 736.20 −1.236 14.470
3 0.389 3.54 × 10−5 3.54 × 10−5 −0.734 721.00 −3.554 32.580
Zn alloy
0.5 0.465 3.12 × 10−5 3.12 × 10−5 −1.047 822.90 −1.756 18.230
1 2.443 1.64 × 10−4 1.64 × 10−4 −1.048 156.70 −1.296 12.410
1.5 3.321 2.23 × 10−4 2.23 × 10−4 −1.042 115.30 −1.118 11.590
2 3.863 2.59 × 10−4 2.59 × 10−4 −1.042 99.12 −1.107 13.700
2.5 4.308 2.89 × 10−4 2.89 × 10−4 −1.048 89.62 −2.402 12.010
3 5.016 3.37 × 10−4 3.37 × 10−4 −1.042 76.35 −0.554 14.430

The anodic reaction involves the diffusion of Zn2+ and Al3+ ions following ionization of the alloy surfaces within the electrolyte [56]. The anodic polarization plots in Figure 1(a) and (b) substantially vary from each other. However, the anodic plots within each figure also vary according to the NaCl concentration. This variation shows the anodic corrosion reaction mechanism is diffusion-controlled. While the plot in Figure 1(b) depicts limited dissolution of the Zn surface due to limited collapse of the inert oxide film initially formed on the alloy before passivation of the alloy [57,58], Al alloy exhibited significant current transient peaks. These peaks signify active-passive transition behavior on the steel surface. The peaks extend to the region where stable pitting initiates for the plots at 1–3% NaCl concentration. A gain in Cl ion concentration causes the substitution of OH ions on the Al surface resulting probably in the interaction of Cl and net progression in corrosion rate as shown in Table 2 [59]. However, the formation of passivating oxide film (Al2O3) during potential scanning strongly influenced the overall reaction processes [60,61,62].

The reaction process in the presence of chloride on the Al surface is summarized by the following equation (equations (6)–(13)):

(6) Al AI 3 + + 3 e ,

(7) AI 3 + + H 2 O Al ( OH ) 2+ + H + ,

(8) AI 3+ + Cl AICI 2+ ,

(9) AI ( OH ) 2+ + Cl AI ( OH ) CI + ,

(10) AICI 2 + + 2 H 2 O AI ( OH ) 2 CI + 2H + ,

(11) AI ( OH ) Cl + + H 2 O Al ( OH ) 2 CI + H + ,

(12) Al ( OH ) 2 CI + H 2 O Al ( OH ) 3 + H + + Cl ,

(13) 2Al ( OH ) 3 ( amorphous ) γ Al 2 O 3 H 2 O ( boehmite ) + 2H 2 O .

Zn alloy displays a stable anodic passivation reaction at all Cl anion concentrations during potential scanning. The analogous anodic reaction process for Zn occurs as follows:

(14) Zn Zn 2+ + 2e .

The strong attraction of Zn alloy for O2 causes strong resistance to active-passive transition behavior at all NaCl concentrations. The passive portion on Zn stretches to the transpassive portion of the anodic plot where pitting corrosion initiates and grows.

Observation of Table 2 shows corrosion rate data for Al and Zn alloys in the neutral chloride solution. Correlation of the data shows Al is more resilient to general corrosion compared to Zn despite significant thermodynamic instability on the Al surface due to current transients. The corrosion rate of Zn started at 0.432 mm/year (0.5% NaCl concentration) analogous to corrosion current density of 2.9 × 10−5 A/cm2 and consistently increased to 0.691 mm/year (3% NaCl concentration) due to the reaction effect of the Cl anions analogous to corrosion current density of 4.63 × 10−5 A/cm2. The increase in Cl anion concentration hastened the resolve of the inert film on Zn alloy such that adsorbed O2 molecules on the metal surface are substituted by Cl anions through aggressive adsorption and removal reactions processes [63]. This exposes the alloy to further corrosion reactions due to the evolution of weak surface precipitates. The corrosion rate of Al alloy initiated at 0.031 mm/year (0.5% NaCl concentration) and consistently increased to 0.085 mm/year at 1.5% NaCl concentration, where it peaked. Beyond 1.5% NaCl concentration, corrosion rate results varied, culminating at 0.082 mm/year consistent with a corrosion current density of 7.48 × 10−6 A/cm2 at 3% NaCl concentration. The limited variation in corrosion rate data for Al shows the threshold Cl anion concentration was attained from 1.5 to 3% NaCl concentration. The threshold values are the product of the redox reactions on the Al surface and the formation of precipitates.

The corrosion polarization plots in Figure 2(a) and (b) substantially vary from the plots in Figure 1(a) and (b) due to the additional presence of SO4 2− anions within the electrolyte. The dual electrochemical interaction of Cl and SO4 2− anions ensured the anodic slope of the polarization curves (Figure 2(a) and (b)) remains high at all Cl anion concentrations. This is due to the collapse of the ionized Al and Zn surfaces. This assertion is proven by the corrosion rate results for Al and Zn in Table 3. The corrosion rate results initiated at values of 0.047 and 0.465 mm/year (0.5% NaCl concentration) and consistently progressed to values of 0.389 and 5.016 mm/year. It is clearly stated that the corrosion rate data for Al and Zn in the chloride-sulfate solution are substantially greater than in the neutral chloride solution, while the corrosion rate results for Zn are substantially greater than the corresponding values for Al. The observation proves the chloride-sulfate solution is much stronger and more aggressive than the neutral chloride solution. Second, the precipitates deposited from the reaction processes of the Cl/SO4 2− anions are more soluble when compared to the precipitates from the neutral chloride media. The substantial rise in corrosion rate for Al in the chloride-sulfate solution occurred at 1.5% NaCl concentration (0.386 mm/year). The reaction of Al with the SO4 2− anion occurs according to the following equations:

(15) Al 3 + + SO 4 2 AlSO 4 2 ,

(16) Al ( OH ) 2 + + SO 4 2 Al ( OH ) SO 4 2 .

Zn2+ reacts with H+ ions and SO4 2− ions with respect to the following equations:

(17) Zn + H 2 SO 4 ZnSO 4 + H 2 .

Zn2+ and 2OH ions react to produce Zn(OH)2 [64].

(18) Zn 2 + + 2OH Zn ( OH ) 2 .

Cl anions transport to anodic sites resulting in the formation of Zn5(OH)8Cl2

(19) 5 Zn ( OH ) 2 + 2 Cl + H 2 O Zn 5 ( OH ) 8 Cl 2 ·H 2 O + 2OH .

The cathodic polarization curves in Figure 2(a) and (b) depict a substantial reduction in the cathodic polarization reaction toward the end of the polarization slope before the intersection with the anodic plot. This is due to a decrease in the H2 evolution and O2 reduction reactions associated with enhanced impedance of the alloy surface and a decrease in the diffusion of reducible species [65]. Significant current transients were visible on the anodic cathodic polarization plot due to passivation reactions associated with the transient collapse and passivation of the protective oxide.

3.2 Passivation and pitting corrosion studies

Potentiostatic data for Al and Zn corrosion in a neutral chloride solution were obtained from the potentiodynamic polarization plots. Table 4 depicts the potentiostatic parameters obtained. Al and Zn are known to form protective oxides on their surface when attacked by corrosive species. This occurs due to the interaction of O2 atoms inside the electrolyte. The inert film suppresses electrochemical reactions at the metal-solution interface [66,67]. The corrosion potential is the value where the proportion of cathodic and anodic mechanisms intersects on the polarization plot and indicates their electrochemical properties. The passivation potential represents the potential where transient corrosion pits disappear due to the passivation of the alloy surface [68]. The stable pitting potential is the value at which corrosion pits initiate and grow without the possibility of collapsing while the passivation range gives an indication of the resilience of the protective oxide. Table 4 shows the Al alloy passivates after anodic polarization without the evolution of transient corrosion pits (metastable pitting). Hence, its passivation is almost instantaneous. However, significant current transients are visible throughout the passivation region. The current transients are the results of breakage and reformation of the protective oxide on the Al surface. Nevertheless, the protective oxide is thermodynamically unstable.

Table 4

Potentiostatic data for passivation and pitting corrosion resilience of Al and Zn corrosion in NaCl media (0.5–3% NaCl concentration)

NaCl concentration (%) Corrosion potential (V) Passivation potential (V) Passivation current (A) Stable pitting potential (V) Passivation range (V)
Al alloy
0.5 −0.925 −0.638 0.287
1 −0.923 −0.644 0.279
1.5 −0.928 −0.656 0.272
2 −0.920 −0.674 0.246
2.5 −0.867 −0.683 0.184
3 −0.814 −0.699 0.115
Zn alloy
0.5 −1.233 −1.200 3.10 × 10−5 −1.010 0.223
1 −1.250 −1.220 2.68 × 10−5 −1.050 0.200
1.5 −1.244 −1.210 3.06 × 10−5 −1.040 0.204
2 −1.240 −1.220 2.70 × 10−5 −1.040 0.200
2.5 −1.251 −1.230 3.84 × 10−5 −1.050 0.201
3 −1.250 −1.230 3.08 × 10−5 −1.050 0.200

Comparing these to the potentiostatic data for Zn alloy, it is evident that limited anodic polarization of the alloy surface occurred before stable passivation of the Zn surface. Metastable pitting activity is completely absent from the polarization plots. The absence of current transients shows the protective oxide is stable though it did not translate to greater corrosion resistance considering the corrosion rate values in Table 2. Zn passivated at potential values ranging from −1.20 V (3.10 × 10−5 A) at 0.5% NaCl to −1.23 V (3.08 × 10−5 A) at 3% NaCl concentration. The alloy passivated at almost the same potential which extended up to the potential for stable pitting (−1.010 to −1.050 V). Al pitted at values ranging from −0.638 V at 0.5% NaCl to −0.699 V at 3% NaCl. The passivation range values for Zn alloy are generally lower than the corresponding values for Al alloy as shown in Table 4 at all NaCl concentrations. This confirms that Al though more thermodynamically unstable at the passivated regions exhibits a protective oxide that is more resilient compared to the oxide on Zn [69]. Cl anion concentration influences the passivation range for Al alloy. The passivation range value for Al decreases from 0.287 V at 0.5% NaCl to 0.115 V at 3% NaCl. This contrasts the observation for Zn alloy where the passivation range values after 0.5% NaCl concentration (0.223 V) were generally stable till 3% NaCl concentration.

3.3 Optical microscopy analysis

Optical representative images of Al and Zn alloys after corrosion in neutral chloride solution at 3% NaCl concentration are revealed in Figure 3(a) and (b) while Figure 4 shows their representative images from the acid chloride solution at 3% NaCl concentration at mag. ×10, ×40 and ×100. In agreement with the corrosion rate results from potentiodynamic polarization, it is clearly visible in Figure 3(a) that localized deterioration occurred on the surface of Al alloy. Localized deterioration occurred along the grain boundary simultaneously with the general surface corrosion. The localized deterioration is responsible for the current transients due to active–passive transition properties of the protective oxide [70]. This phenomenon proves the resilience of the oxide film. However, under-induced potential corrosion will eventually occur. Comparing this to the optical image in Figure 3(b), it is established that Zn underwent general surface deterioration. The effect of localized corrosion is negligible. This is due to the microstructural and metallurgical properties of Zn which significantly differs from Al alloy. The extent of localized surface deterioration on Al increased in the presence of combined Cl and SO4 2− anions as shown in Figure 4(a). Adsorbed O2 atoms responsible for the formation of Al2O3 were displaced by the corrosive anions which exposed the substrate Al alloy to corrosion. This observation also applies to Zn as depicted in Figure 4(b) where the degree of general surface deterioration is much higher.

Figure 3 
                  Optical representative images of (a) Al alloy and (b) Zn alloy before corrosion test.
Figure 3

Optical representative images of (a) Al alloy and (b) Zn alloy before corrosion test.

Figure 4 
                  Optical representative images of (a) Al alloy and (b) Zn alloy from neutral chloride solution at 3% NaCl concentration.
Figure 4

Optical representative images of (a) Al alloy and (b) Zn alloy from neutral chloride solution at 3% NaCl concentration.

3.4 Open circuit potential analysis

Open circuit potential plots for Al and Zn at 0.5% and 3% NaCl concentrations from the neutral chloride and acid-chloride solutions were produced as shown in Figures 5(a) and (b). In agreement with the results from potentiodynamic polarization test, Figure 5(a) shows Al alloy in neutral chloride solution displayed greater corrosion resilience and increased protective oxide evolution during potential monitoring. The plot at 0.5% NaCl concentration initiated at −1.216 V (0 s), a significant electronegative value due to its amphoteric nature. The surface characteristics of the Al results in spontaneous electrochemical reactions, i.e. instantaneous collapse and subsequent repassivation of the protective oxide. Electropositive shift of the OCP plot occurred to 901.8 s (−0.524 V). It must be noted that the shift is due to the growth of Al2O3 on Al alloy [71]. The competitive reaction of O2 and Cl ionic species results on the alloy surface results in adsorption of O2 atoms responsible for oxide formation. Though this observation is specific to 0.5% NaCl concentration. Beyond 900 s of exposure, the OCP plot for Al is relatively stable, but the potential transients show the electrochemical properties of the protective oxide is unstable till 7,200 s at −0.399 V. Comparing these observations to the plot at 3% NaCl concentration, it is very probable that increase in Cl anion concentration increased the corrosion tendency of the Al alloy as depicted in the plot configuration [Figure 6(a)]. The electropositive shift associated with Al at 5% NaCl concentration has significantly decreased. The plot at 3% NaCl concentration initiated at −0.844 (0 s), underwent a minor electronegative shift till −0.948 V at 269.6 s before shifting electropositively to −0.801 V at 808.21 s. Henceforth, from this value, the OCP plot was thermodynamically stable till −0.771 V at 7,200 s. It is also visible that the potential transients have decreased.

Figure 5 
                  Optical representative images of (a) Al alloy and (b) Zn alloy from acid-chloride solution at 3% NaCl concentration.
Figure 5

Optical representative images of (a) Al alloy and (b) Zn alloy from acid-chloride solution at 3% NaCl concentration.

Figure 6 
                  OCP Plot for Al and Zn alloys in (a) neutral chloride solution and (b) acid-chloride solution at 0.5 and 3% NaCl concentration.
Figure 6

OCP Plot for Al and Zn alloys in (a) neutral chloride solution and (b) acid-chloride solution at 0.5 and 3% NaCl concentration.

Comparing the thermodynamic behavior of Al to Zn in NaCl, Zn at 0.5, and 3% NaCl concentration displayed the same OCP plot configuration. The plots initiated at −1.205 and −1.268 V shifted electropositively before reaching thermodynamic equilibrium at −0.929 V (132.4 s) and −1.007 V (282.8 s). The corrosion rate values at 7,200 s are −0.977 and −0.996 V which is significantly more electronegative than the corresponding values for Al alloy. However, potential transients are completely absent due to the stability of the protective oxide on Zn in spite of its higher corrosion tendency. The plot configuration for Zn in the acid-chloride solution at 0.5 and 3% NaCl concentration [Figure 6(b)] was usually the same as that of Zn in the neutral chloride solution [Figure 6(a)]. The OCP values started at −1.03 and −1.24 V (0 s) and underwent a sharp electropositive shift to −0.990 V at 200 s. After this section, the OCP plot was generally constant till −0.96 and −0.98 V at 7,200 s. In the presence of the combined electrochemical influence of Cl and SO4 2− anions, the electrochemical properties of the Zn surface were generally stable. The OCP plot for Al in the acid-chloride solution exhibited substantial potential transient throughout. The degree of instability is much higher for the Al plot at 3% NaCl concentration. Both plots (Al at 0.5 and 3% NaCl concentration) initiated at −0.684 and −0.753 V (0 s) and terminated at −0.602 and −0.666 V (7,200 s)

4 Conclusion

Analysis of the corrosion resistance and passivation behavior of aluminum and zinc alloys in neutral chloride and acid chloride solutions shows the protective oxide on aluminum is more resilient to general and localized deterioration in the presence of Cl and SO4 2− anions. The corrosion potential of zinc polarization plots was significantly more electronegative compared to the values for aluminum. The passivation range values for aluminum were significantly wider than the values for zinc despite visible thermodynamic instability. Data from open circuit potential measurement show significant formation and growth of the protective oxide aluminum which is responsible for its higher corrosion resistance compared to zinc. Zinc alloy despite its lower corrosion resistance compared to aluminum exhibited thinner and less resilient oxide formation which exhibits more thermodynamic stability. Localized deterioration occurred along the grain boundary simultaneously with the general surface corrosion on the surface of Al alloy. The deterioration is responsible for the significant current transients on the polarization plots. Zn underwent general surface deterioration which became more adverse in the presence of Cl/SO4 2− anions. This phenomenon is due to differences in the microstructural and metallurgical properties of Zn compared to Al alloy.

Acknowledgement

The author is grateful to Covenant University for their financial support and provision of facilities towards the success of this research.

  1. Conflict of interest: Author states no conflict of interest.

  2. Data availability statement: The datasets generated during and/or analysed during the current study are available from the corresponding author on reasonable request.

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Received: 2023-07-30
Revised: 2023-09-23
Accepted: 2023-10-01
Published Online: 2024-01-24

© 2024 the author(s), published by De Gruyter

This work is licensed under the Creative Commons Attribution 4.0 International License.

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  116. Investigated of the optical properties for SiO2 by using Lorentz model
  117. Measurements of induced vibrations due to steel pipe pile driving in Al-Fao soil: Effect of partial end closure
  118. Experimental and numerical studies of ballistic resistance of hybrid sandwich composite body armor
  119. Evaluation of clay layer presence on shallow foundation settlement in dry sand under an earthquake
  120. Optimal design of mechanical performances of asphalt mixtures comprising nano-clay additives
  121. Advancing seismic performance: Isolators, TMDs, and multi-level strategies in reinforced concrete buildings
  122. Predicted evaporation in Basrah using artificial neural networks
  123. Energy management system for a small town to enhance quality of life
  124. Numerical study on entropy minimization in pipes with helical airfoil and CuO nanoparticle integration
  125. Equations and methodologies of inlet drainage system discharge coefficients: A review
  126. Thermal buckling analysis for hybrid and composite laminated plate by using new displacement function
  127. Investigation into the mechanical and thermal properties of lightweight mortar using commercial beads or recycled expanded polystyrene
  128. Experimental and theoretical analysis of single-jet column and concrete column using double-jet grouting technique applied at Al-Rashdia site
  129. The impact of incorporating waste materials on the mechanical and physical characteristics of tile adhesive materials
  130. Seismic resilience: Innovations in structural engineering for earthquake-prone areas
  131. Automatic human identification using fingerprint images based on Gabor filter and SIFT features fusion
  132. Performance of GRKM-method for solving classes of ordinary and partial differential equations of sixth-orders
  133. Visible light-boosted photodegradation activity of Ag–AgVO3/Zn0.5Mn0.5Fe2O4 supported heterojunctions for effective degradation of organic contaminates
  134. Production of sustainable concrete with treated cement kiln dust and iron slag waste aggregate
  135. Key effects on the structural behavior of fiber-reinforced lightweight concrete-ribbed slabs: A review
  136. A comparative analysis of the energy dissipation efficiency of various piano key weir types
  137. Special Issue: Transport 2022 - Part II
  138. Variability in road surface temperature in urban road network – A case study making use of mobile measurements
  139. Special Issue: BCEE5-2023
  140. Evaluation of reclaimed asphalt mixtures rejuvenated with waste engine oil to resist rutting deformation
  141. Assessment of potential resistance to moisture damage and fatigue cracks of asphalt mixture modified with ground granulated blast furnace slag
  142. Investigating seismic response in adjacent structures: A study on the impact of buildings’ orientation and distance considering soil–structure interaction
  143. Improvement of porosity of mortar using polyethylene glycol pre-polymer-impregnated mortar
  144. Three-dimensional analysis of steel beam-column bolted connections
  145. Assessment of agricultural drought in Iraq employing Landsat and MODIS imagery
  146. Performance evaluation of grouted porous asphalt concrete
  147. Optimization of local modified metakaolin-based geopolymer concrete by Taguchi method
  148. Effect of waste tire products on some characteristics of roller-compacted concrete
  149. Studying the lateral displacement of retaining wall supporting sandy soil under dynamic loads
  150. Seismic performance evaluation of concrete buttress dram (Dynamic linear analysis)
  151. Behavior of soil reinforced with micropiles
  152. Possibility of production high strength lightweight concrete containing organic waste aggregate and recycled steel fibers
  153. An investigation of self-sensing and mechanical properties of smart engineered cementitious composites reinforced with functional materials
  154. Forecasting changes in precipitation and temperatures of a regional watershed in Northern Iraq using LARS-WG model
  155. Experimental investigation of dynamic soil properties for modeling energy-absorbing layers
  156. Numerical investigation of the effect of longitudinal steel reinforcement ratio on the ductility of concrete beams
  157. An experimental study on the tensile properties of reinforced asphalt pavement
  158. Self-sensing behavior of hot asphalt mixture with steel fiber-based additive
  159. Behavior of ultra-high-performance concrete deep beams reinforced by basalt fibers
  160. Optimizing asphalt binder performance with various PET types
  161. Investigation of the hydraulic characteristics and homogeneity of the microstructure of the air voids in the sustainable rigid pavement
  162. Enhanced biogas production from municipal solid waste via digestion with cow manure: A case study
  163. Special Issue: AESMT-7 - Part I
  164. Preparation and investigation of cobalt nanoparticles by laser ablation: Structure, linear, and nonlinear optical properties
  165. Seismic analysis of RC building with plan irregularity in Baghdad/Iraq to obtain the optimal behavior
  166. The effect of urban environment on large-scale path loss model’s main parameters for mmWave 5G mobile network in Iraq
  167. Formatting a questionnaire for the quality control of river bank roads
  168. Vibration suppression of smart composite beam using model predictive controller
  169. Machine learning-based compressive strength estimation in nanomaterial-modified lightweight concrete
  170. In-depth analysis of critical factors affecting Iraqi construction projects performance
  171. Behavior of container berth structure under the influence of environmental and operational loads
  172. Energy absorption and impact response of ballistic resistance laminate
  173. Effect of water-absorbent polymer balls in internal curing on punching shear behavior of bubble slabs
  174. Effect of surface roughness on interface shear strength parameters of sandy soils
  175. Evaluating the interaction for embedded H-steel section in normal concrete under monotonic and repeated loads
  176. Estimation of the settlement of pile head using ANN and multivariate linear regression based on the results of load transfer method
  177. Enhancing communication: Deep learning for Arabic sign language translation
  178. A review of recent studies of both heat pipe and evaporative cooling in passive heat recovery
  179. Effect of nano-silica on the mechanical properties of LWC
  180. An experimental study of some mechanical properties and absorption for polymer-modified cement mortar modified with superplasticizer
  181. Digital beamforming enhancement with LSTM-based deep learning for millimeter wave transmission
  182. Developing an efficient planning process for heritage buildings maintenance in Iraq
  183. Design and optimization of two-stage controller for three-phase multi-converter/multi-machine electric vehicle
  184. Evaluation of microstructure and mechanical properties of Al1050/Al2O3/Gr composite processed by forming operation ECAP
  185. Calculations of mass stopping power and range of protons in organic compounds (CH3OH, CH2O, and CO2) at energy range of 0.01–1,000 MeV
  186. Investigation of in vitro behavior of composite coating hydroxyapatite-nano silver on 316L stainless steel substrate by electrophoretic technic for biomedical tools
  187. A review: Enhancing tribological properties of journal bearings composite materials
  188. Improvements in the randomness and security of digital currency using the photon sponge hash function through Maiorana–McFarland S-box replacement
  189. Design a new scheme for image security using a deep learning technique of hierarchical parameters
  190. Special Issue: ICES 2023
  191. Comparative geotechnical analysis for ultimate bearing capacity of precast concrete piles using cone resistance measurements
  192. Visualizing sustainable rainwater harvesting: A case study of Karbala Province
  193. Geogrid reinforcement for improving bearing capacity and stability of square foundations
  194. Evaluation of the effluent concentrations of Karbala wastewater treatment plant using reliability analysis
  195. Adsorbent made with inexpensive, local resources
  196. Effect of drain pipes on seepage and slope stability through a zoned earth dam
  197. Sediment accumulation in an 8 inch sewer pipe for a sample of various particles obtained from the streets of Karbala city, Iraq
  198. Special Issue: IETAS 2024 - Part I
  199. Analyzing the impact of transfer learning on explanation accuracy in deep learning-based ECG recognition systems
  200. Effect of scale factor on the dynamic response of frame foundations
  201. Improving multi-object detection and tracking with deep learning, DeepSORT, and frame cancellation techniques
  202. The impact of using prestressed CFRP bars on the development of flexural strength
  203. Assessment of surface hardness and impact strength of denture base resins reinforced with silver–titanium dioxide and silver–zirconium dioxide nanoparticles: In vitro study
  204. A data augmentation approach to enhance breast cancer detection using generative adversarial and artificial neural networks
  205. Modification of the 5D Lorenz chaotic map with fuzzy numbers for video encryption in cloud computing
  206. Special Issue: 51st KKBN - Part I
  207. Evaluation of static bending caused damage of glass-fiber composite structure using terahertz inspection
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