International Journal of Corrosion
Volume 2018 (2018), Article ID 2381287, 15 pages
https://doi.org/10.1155/2018/2381287

Research Article

The Red Sea as a Corrosive Environment: Corrosion Rates and Corrosion Mechanism of Aluminum Alloys 7075, 2024, and 6061

Aisha H. Al-Moubaraki and Hind H. Al-Rushud

Chemistry Department, Faculty of Sciences, King Abdulaziz University, Al Faisaliah Campus, Jeddah, Saudi Arabia

Correspondence should be addressed to Aisha H. Al-Moubaraki; ahm13988@hotmail.com

Received 4 November 2017; Revised 14 February 2018; Accepted 4 March 2018; Published 21 May 2018

Academic Editor: Jerzy A. Szpunar

Copyright © 2018 Aisha H. Al-Moubaraki and Hind H. Al-Rushud. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Abstract.

Corrosion behavior of Al 7075, Al 2024, and Al 6061 in the Red Sea water was studied using weight loss (WL) measurements and potentiodynamic polarization (PDP) technique. The corrosion patterns and corrosion products formed on Al alloys were characterized using optical photography (OP), scanning electron microscopy (SEM), and energy-dispersive spectroscopy (EDS). The results showed that WL data were consistent with bimodal model rather than the power law function and the corrosion rates exhibit a continuous decrease with exposure time. The increasing order of the Red Sea corrosivity on the studied Al alloys can be given as follows: Al 6061 < Al 2024 < Al 7075. The results of temperature effect revealed that an increase in temperature resulted in an increase in both anodic and cathodic current density and a decrease in corrosion potential. Al 7075 was less influenced by temperature than the other alloys. Pitting corrosion was the predominant corrosion pattern detected on all Al alloy surfaces after prolonged immersion in the Red Sea water. The appearance of S peak in EDS spectra of Al 7075 after corrosion gives an indication of the contribution of bacteria in the corrosion process.

1. Introduction

Desirable properties of aluminum such as low density (only 2.7 g/cm³), recyclability, thermal and electrical conductivity, and, in some degree, corrosion resistance, make aluminum the most consumed nonferrous metal in the world [1]. Aluminum is often alloyed with other elements to improve its mechanical properties and increase its usefulness [2]. Commercially wrought aluminum alloys are classified into different series depending on their principle alloying elements such as 2xxx (Al-Cu alloys), 5xxx (Al-Mg alloys), 6xxx (Al-Mg-Si alloys), and 7xxx series (Al-Zn-Cu alloys). Wrought aluminum alloys are used in marine engineering applications, specifically 5xxx and 6xxx series, as in shipbuilding, coastal equipment, and desalination of seawater [3–5]. In fact, aluminum alloys have less corrosion resistance than pure metal; so, they are often used with an appropriate protection method [2, 3].

Corrosion is defined by ISO as “physicochemical interaction (usually of an electrochemical nature) between a metal and its environment which results in changes in the properties of the metal and which often leads to impairment of the function of the metal, the environment, or the technical system of which these form a part” [6]. From a thermodynamic view, a layer of aluminum oxide is formed on aluminum surface in pH ranges of 4 to 9, acting as a physical barrier that separates aluminum from its environment and prevents further dissolution; but, the stability of the oxide layer can be influenced by the presence of aggressive anions in the environment such as chloride in seawater [7, 8]. The properties of the protective oxide film can also be affected by alloying elements. Those alloying elements are present not only in aluminum solid solution but also in intermetallic (IM) particles. The microstructures of aluminum alloys are complex and highly heterogeneous compared to other alloys [9]. IM particles are randomly distributed in the alloys matrix and have different microstructures and composition than the solid solution. As a result, they have different electrochemical potentials which produce an opportunity to create microgalvanic cells between these particles and the aluminum matrix [10, 11]. Both the heterogeneous nature of alloys and presence of aggressive anions in the environments can cause loss of passivity at specific sites of aluminum alloy surface and lead to localized corrosion [7, 12, 13]. Muller and Galvele [14] studied the role of alloying elements in pitting corrosion of Al-Zn, Al-Cu, and Al-Mg binary alloys in 1 M NaCl. It was observed that pitting potential decreased with increase in Zn content up to 3%, addition of copper increased pitting potential dramatically up to 5%, and Mg did not affect the pitting potential.

Various environmental factors such as dissolved gases, temperature, pH, and micro- and macroorganisms can affect corrosion in seawater [15, 16]. Most of these factors are interrelated with each other as an increase in temperature will reduce the dissolved oxygen and result in a change in biological activities; thus, evaluation of the corrosion process in seawater is complicated. Dissolved oxygen is an important factor because oxygen reduction is a primary cathodic reduction for corrosion of Al alloys in seawater [17]. Aluminum and its alloys have been reported to experience microbial influenced corrosion (MIC). Sulfate reducing bacteria (SRB) present in seawater is the most widely known and studied as the cause of MIC. SRB form tubercles (discrete hemispherical mounds) on aluminum surface and enhance pitting corrosion as a result of low pH of electrolyte under tubercles [18, 19]. In corrosion studies, seawater is often duplicated by 3.5 NaCl but salt concentration is not efficient to duplicate the properties of natural seawater. However, many researchers have studied the corrosion behavior of aluminum alloys in natural seawater and their results revealed that aluminum and its alloys mainly suffered from pitting corrosion in seawater [20–22]. In previous studies on aluminum corrosion by pitting, researchers distinguished between crystallographic and alkaline pitting. When cathodic intermetallic particles enhance the dissolution of the surrounding matrix, it is called alkaline pits. This type of pitting occurs below the pitting potential, while crystallographic pits are formed when an alloy reaches its pitting potential [23].

Using three different aluminum alloys (Al 7075, Al 2024, and Al 6061), the present research studied the Red Sea as a corrosive environment. Factors such as immersion time and temperatures on the corrosion behavior of aluminum alloys in seawater were studied using weight loss (WL) and potentiodynamic polarization (PDP) measurements. Change in aluminum alloy surfaces was detected at different conditions using optical photography (OP), scanning electron microscope (SEM), and electron-dispersive energy spectroscopy (EDS).

2. Materials and Methods

2.1. Materials

Three different types of aluminum alloys were used in this study. The chemical composition of aluminum alloys is given in Table 1. Specimens, 10 to 15 mm in diameter and 40 to 50 mm in length, were cut from the respective metal rods. Prior to each experiment, the exposed surfaces were scratched with a series of emery paper from 80 to 1200 grades. Then, they were washed several times with deionized water and then with ethanol and finally dried using a stream of air. The specimens were then weighed accurately and immersed in the test solution. The test solution was natural seawater and it was collected directly from the Red Sea in the western region (Obhur, Jeddah, Saudi Arabia). Several properties of the sample such as pH, electrical conductivity, total alkalinity, and content of different ions were demonstrated in previous work [24].

Table 1: Percentage composition of the studied Al alloys.

Alloy
Cr
Cu
Fe
Mg
Mn
Si
Ti
Zn
Zr
Al

7075
0.18–0.28
1.2–2.0
0.5
2.1–2.9
0.3
0.4
0.2
5.1–6.1
0.25
Remainder

2024
0.10
3.8–4.9
0.5
1.2–1.8
0.3–0.9
0.5
0.15
0.25
-
Remainder

6061
0.04–0.35
0.15–0.4
0.7
0.8–1.2
0.15
0.4–0.8
0.15
0.25
-
Remainder

2.2. Methods

2.2.1. Weight Loss (WL)

Polished and preweighed Al specimens were placed in airtight glass containers containing 60 mL of seawater for different immersion periods (1, 2, 3, 5, 7, 10, 22, and 32 weeks) at an ambient temperature (laboratory temperature was 21 ± 1°C) under stagnant conditions. To facilitate the identification of specimens immersed in the seawater at different conditions, numbered stickers were used in each case (Figure 1). At the end of each immersion period, the specimens were assessed by weight loss measurement. Layers of corrosion products were scraped off the Al surfaces with a bristle brush and immediately immersed in the pickling solution containing concentrated nitric acid (86%) for five minutes (ASTM G1) [25]. After corrosion products were completely removed, the specimens were rinsed with deionized water and ethanol, dried with a stream of air, and reweighed to determine weight loss. Duplicate experiments were conducted for all the weight loss experiments. The corrosion rate was calculated in g/m² year according to the following equation:

where is weight loss in grams (g), is area in square meters (m²), and is the exposure time in year.

Figure 1: The final arrangement for weight loss experiments.

2.2.2. Potentiodynamic Polarization (PDP)

Potentiodynamic polarization measurements were performed in a three-electrode cell. A cylinder specimen of Al alloys was used as working electrode and was embedded in a Teflon holder using epoxy resin, giving an exposed area of 0.699 to 1.269 cm². Platinum mesh was used as the counter electrode and silver/silver chloride (Ag/AgCl(s)/KCl saturated (aq)) was used as the reference electrode. Potentiodynamic polarization measurements were done using ACM Gill AC Potentiostat/Galvanostat model 1649 connected to a personal computer. Prior to each experiment, the working electrode was treated as described in the weight loss method and then dipped in the test solution. After reaching a steady-state potential, the potentiodynamic curves were carried out by changing, linearly, the electrode potential from the starting potential (−1200 mV) with respect to the reference electrode towards a less negative direction with the required scan rate (1 mV/s) till the end of the experiment at −200 mV. All the electrochemical measurements were done twice at different conditions. Corrosion current densities were determined by extrapolation of cathodic Tafel line to corrosion potential using the ACM Gill software.

2.3. Surface Examination Study

2.3.1. Optical Photograph

Optical photographs of Al alloy specimens were taken after the chemical experiments, to evaluate gross changes in the metal surface and to perform a cursory evaluation of the forms of corrosion (e.g., general, pitting) at different conditions. Optical photographs were taken using VMS-004 USB microscope.

2.3.2. SEM-EDS Measurement

The scanning electron microscopy (SEM) associated with the energy-dispersive X-ray spectroscopy (EDS) was used to investigate the surface morphology of aluminum alloys and analyze the elements on the surfaces of alloys before and after immersion in seawater for five weeks.

3. Results and Discussion

3.1. Weight Loss

3.1.1. Time Dependence of Corrosion Rate

Table 2 and Figure 2 give the weight loss and corrosion rates of Al alloys at different immersion periods in the Red Sea water. The results showed that weight loss increased (Figure 2(a)), while the corrosion rates decreased (Figure 2(b)) with increase in time of exposure. Decrease in corrosion rates with time is frequently observed in many types of environments [26–28] and is caused by the gradual build-up of a thicker and more protective layer. This layer is not truly passivating as it acts as a membrane, especially in the presence of aggressive ions such as the Cl⁻ ions. If Cl⁻ ions are present in the aqueous phase, they can penetrate the corrosion product layer and corrode the Al alloys (increase in weight loss value), although at a reduced rate [24]. The results indicate that the CRs depend on the composition of the studied Al alloys. Sinyavskii and Kalinin [21] reported that if cathodic additives and impurities in aluminum alloys such as Cu and Fe increase, the susceptibility to localized corrosion increases. This explains the poor corrosion resistance of Al 7075 and Al 2024 and high corrosion resistance of Al 6061 alloy. Zinc content in Al 7075 reduced its corrosion resistance and led to higher corrosion rate. According to the corrosion rates values, the increasing order of the Red Sea water corrosivity on the studied Al alloys can be given as follows.

Corrosion pattern can be monitored at different periods by visual inspection as shown in Figures 3–5. It is obvious that the alloys suffered from localized corrosion, especially pitting form. Deep and shallow pits appeared on the Al alloy surface. The samples with pitting corrosion had white sediment of corrosion products above every pit. Around the pits, there was a brighter area, which is the cathodic area where the reduction occurs. The color of the surface, the number of pits, and the spread of the pits were different for each alloy and different immersion periods. The Red Sea has a high concentration of chloride ions and according to Frankel [28], pitting corrosion will only occur in the presence of aggressive anionic species, and chloride ions are usually the cause. The severity of pitting tends to vary with the logarithm of the bulk chloride concentration [7]. The aggressiveness of chloride anion is attributed to its ability to interfere with passivation as it is a small anion with high diffusivity

Table 2: Weight loss and corrosion rates of Al alloys at different immersion periods in the Red Sea water.

Immersion period (weeks)
Weight loss (g m⁻²)
Corrosion rate, (g m⁻² year⁻¹)

Al 7075
Al 2024
Al 6061
Al 7075
Al 2024
Al 6061

1st
0.733
0.463
0.312
38.184
24.111
16.247

2nd
1.227
0.781
0.539
31.956
20.328
14.034

3rd
1.685
0.820
0.648
29.313
14.269
11.268

5th
2.284
1.721
0.997
23.813
17.950
10.392

7th
2.366
1.891
1.094
17.630
14.088
8.150

10th
2.396
1.994
1.147
12.490
10.394
5.981

22nd
3.826
2.567
1.663
9.069
6.084
3.942

32nd
4.173
3.241
1.880
6.796
5.279
3.062

(a)

(b)

Figure 2: Dependence of weight loss and corrosion rates of Al alloys in the Red Sea water on immersion time.

Figure 3: Visual images of Al 7075 specimens after immersion in the Red Sea water at different time intervals.

Figure 4: Visual images of Al 2024 specimens after immersion in the Red Sea water at different time intervals.

Figure 5: Visual images of Al 6061 specimens after immersion in the Red Sea water at different time intervals.

3.1.2. Kinetic Study

Most of the previous data sets in corrosion studies appeared to fit the power law function (see (3)) which is derived based on the oxygen diffusion mathematics by Tammann [29]:

where is corrosion loss or pit depth, is exposure time, and and are constants obtained from fitting the function to data. However, a power model involving logarithmic transformation of the immersion time and corrosion loss must be applied in order to obtain the linear form of the above equation as follows:

Figure 6 shows log-log plots for weight loss (g m⁻²) of Al 7075, Al 2024, and Al 6061, respectively, with immersion periods. The data trends of the studied alloys did not show a good fit to a straight line, so they are inconsistent with the power law function model. Melchers [30, 31] reviewed the data sets for long-term corrosion of aluminum and reported that the bimodal model appears to be applicable to long-term corrosion and the power law function is only limited to the short-term corrosion loss. The bilinear graph obtained on log-log coordinates as an alternative obeys an equation of the following type [32, 33]:

where is the weight loss after years, is the first year weight loss, is the duration (in years) of the first exposure period, whose slope is , and is the slope of the second period. One possible reason for this extraordinary behavior may lie in the formation with time of more compact layers which impede the diffusion of the reactive species that participate in the corrosion reactions. However, even though the immersion time in the current experiments did not exceed 32 weeks, the data showed that two distinct lines provide a better fit for the data of Al alloys than a single trend line and this is consistent with the bimodal model. The values of , , , and correlation coefficients ( and ) are estimated and recorded in Table 3.

Table 3: Corrosion kinetic parameters for Al alloys in the Red Sea water.

Kinetic parameters
Al 7075
Al 2024
Al 6061

(g )
12.505
9.029
5.136

0.71
0.763
0.706

0.420
0.326
0.355

0.997
0.920
0.992

0.952
0.964
0.978

Figure 6: versus log for Al alloys immersed in the Red Sea water.

By examining the data obtained in Table 3, the following observations were obtained:

(a)The values of weight loss after one year () indicate that the corrosion of Al alloys in the Red Sea water continues to increase significantly in the same order; Al 7075 is the highest mass loss more frequently, while Al 6061 is the lowest mass loss.(b)The value of can assist as an investigative tool to indicate the diffusion properties through the corrosion products that formed on the metal surface. It was found that the values of are much smaller than that of . The values of can be interpreted according to the following situations [33]:

(i)When is roughly equal to 0.5, the corrosion process is controlled by ideal diffusion process through the corrosion products that remain on the metal surface.(ii)When is greater than 0.5, the diffusion process is accelerated due to corrosion products detachment by cracking, dissolution, soluble complex formation, and so on.(iii)When is less than 0.5, the diffusion process is decreased because the corrosion products layer becomes more compact and protective on the metal surface with time.

The reason for this observation can be stated after considering the proposed mechanism of the bimodal behavior.

According to the above equations, reduction of oxygen and hydrogen ion is the two possible cathodic reactions. In fact, they cannot occur at the same environment conditions. For oxygen reduction, sufficient amount of oxygen must be supplied to the corroded surfaces, whereas hydrogen ion reduction can occur under anoxic conditions. Melchers Centre [30, 31] claimed that continuous formation of corrosion products and nonuniform topography of the corroded surface creates localized anoxic environments and permits hydrogen ion reduction. As the corrosion process progresses with time, the primary cathodic reaction changes to be hydrogen ion reduction instead of oxygen reduction. This change in cathodic reaction and, as a result, in the rate determining step, is the cause of the bimodal trend. Figure 7 shows the schematic bimodal model for corrosion loss as a function of exposure time [31]. As the first trend, a gradual decrease in corrosion rate was observed and this behavior is also represented by the power law function. The nonuniform and nonhomogeneous topography of corroding surfaces will develop as corrosion proceeds, though the thickness and properties of corrosion products on the corroding surfaces and over the pits also become nonuniform. As a result, local regions with low oxygen concentration will be produced and differential aeration cells will be established. These are sufficient conditions for the initiation and progression of pitting corrosion. Oxygen reduction is likely to occur in the shallower regions and corrosion is controlled by inward oxygen diffusion through corrosion products. As the second trend, further build-up of corrosion products will develop highly localized anoxic conditions, especially at the deeper corroded parts (pits). Hydrogen ion reduction is permitted thermodynamically under anoxic condition. In this case, corrosion rate is controlled by the outward diffusion of hydrogen gas. Hydrogen gas diffuses faster than oxygen through corrosion products (because hydrogen molecules are smaller than oxygen molecules) and an increase in corrosion rate is expected if the hydrogen ion reduction becomes the cathodic reaction in sufficient number of areas; this change in the rate trend causes the inflection in the bimodal model. In steady state, hydrogen diffusion cannot remain the rate limiting step for a long time. Other aspects have been considered as reason for the polarized equation (7). This causes a slow decline in instantaneous corrosion rate for longer term exposure such as the inward diffusion of water through the corrosion product, the outward diffusion of soluble corrosion products, or, less likely, the kinetics of the reactions. A review of the previous data revealed that a long period of time (Figure 7 line ) was required to permit deviation from the first trend; so, the short-term corrosion loss of data did not reach this time and was consistent with the power law function. This time can be affected by temperature, oxygen concentrations, or experimental conditions. In the current study, the weight loss experiments were carried out under stagnant conditions at laboratory temperature; this procedure kept corrosion products adherent on the alloy surfaces and high amount of corrosion products accumulated quickly on the corroded surfaces. As a result, the required time to reach the inflection point was reduced to a few weeks. This may be the reason for the observation of the bimodal model with short-immersion corrosion loss.

Figure 7: Schematic bimodal model for long-term corrosion loss and pit depth in marine environments. The change from mode 1 with predominantly oxic corrosion conditions to mode 2 with predominantly anoxic conditions occurs at .

3.2. Potentiodynamic Polarization (PDP)

3.2.1. Effect of Immersion Time

Anodic curves can present useful information on passivation or depassivation of a metal dipped in solutions containing aggressive ions [34, 35]. Figure 8 shows the polarization curves for Al 7075, Al 2024, and Al 6061, respectively, in the Red Sea water after different immersion periods. Al 6061 and Al 2024 show well-defined breakdown potential at all immersion times. Passivity region or difference between corrosion potential and breakdown potential broaden as immersion time increased which may be as a result of accumulation of corrosion products during immersion and build-up of insoluble products. Polarization curves of Al 7075 (2, 24, and 72 h) show a sharp increase in the current density directly above corrosion potential. In this case, the corrosion potential of Al 7075 was often remarked as the first breakdown potential [36]. As the immersion time increased (168 h), the anodic curve of Al 7075 exhibited small passive window and the breakdown potential was distinguished from the corrosion potential. Cathodic curves of the studied alloys shifted to less current at 72 and 168 h of immersion, but the shape of the cathodic curves did not change; thus, it is expected that the cathodic reaction mechanism remains the same over all immersion times. The electrochemical parameters such as and were estimated and listed in Table 4. The influence of immersion time on the above electrochemical parameters is discussed in the following.

(i)The values of tend to increase as immersion time increases, up to a maximum time of 24 h and then tend to decrease at immersion time more than 24 h, as shown in Figure 9(a). The decrease in with immersion time may be attributed to the formation of a protective layer of corrosion products, composed of mainly less soluble aluminum compounds. According to values, Al 7075 has the highest corrosion current, while Al 6061 has the lowest corrosion current density at all immersion times. They resist corrosion in an order like that obtained previously from chemical studies:

(ii)Figure 9(b) shows no definite trend for values. Although the corrosion products are quickly formed on the Al surface, they take a considerably longer time to reach a steady state which is not seen in PDP measurements. The times of immersion included in the PDP study are not sufficient to reach steady state.

Table 4: Potentiodynamic polarization parameters of Al alloys in the Red Sea water at different immersion periods.

Time (hours)
Al 7075
Al 2024
Al 6061

(mV)
(μA/cm²)
(mV)
(μA/cm²)
(mV)
(μA/cm²)

2
732
5.78
842
3.20
814
1.38

24
731
6.29
757
4.31
773
2.28

72
735
2.14
777
1.56
855
1.28

168
806
1.64
777
1.19
749
0.27

Figure 8: Potentiodynamic polarization curves of Al alloys in the Red Sea water at different time interval.

(a)

(b)

Figure 9: Variation of (a) and (b) with immersion periods.

3.2.2. Effect of Temperature

Polarization curves of Al 7075, Al 2024, and Al 6061 immersed in the Red Sea water for 2 h were recorded as a function of temperature and are presented in Figure 10. Temperature affects chemical kinetics of the corrosion reaction and enhances cathodic reaction by increasing oxygen diffusion. The examination of polarization responses of aluminum alloys revealed a continuous increase in both anodic and cathodic current density and a decrease in corrosion potential with increase in temperature. Table 5 shows corrosion potential and breakdown potential of the studied alloys at different temperatures.

Table 5: Corrosion potential (mV) and breakdown potential (mV) of aluminum alloys at different temperature.

Temperature (°C)
Al 7075
Al 2024
Al 6061

(mV)
(mV)
(mV)
(mV)
(mV)
(mV)

10
715
-
797
708
781
700

25
732
-
842
708
814
695

45
793
691
909
704
978
689

60
956
685
968
677
1035
628

Figure 10: Potentiodynamic polarization curves of Al alloys in the Red Sea water at different temperatures.

The obtained results can be interpreted as follows:

(i) values shifted to more negative values with increase in temperatures, indicating that, with increase in the Red Sea water temperatures, the corrosion process comes under cathodic control. Increasing the temperature will increase the rate of oxygen diffusion to the metal surface, thus increasing corrosion current density (Figure 11(a)) because more oxygen is available for the cathodic reduction process. In the current study, this fact did not conflict with the fact that increasing temperature reduces oxygen solubility, because the studied temperatures did not exceed 80°C and the studied systems are closed, whereby oxygen was unable to escape; so, corrosion continued to increase with temperature [37].(ii)It is shown that lowering corrosion potentials was accompanied by raising breakdown potential which resulted in expanding the passive region ΔE of all alloys (Figure 11(b)), especially at high temperatures (45°C and 60°C). Increasing passivation with temperatures was also reported in a previous work [38]. However, increase in passivity region did not result in decrease in the current density. Immersion of alloys in the Red Sea water for 2 h at high temperature resulted in high reaction rate and formation of more amounts of corrosion products. Since a thick barrier of corrosion products is considered as a type of passivation [18], the presence of more corrosion products on alloys surfaces may be the reason for promoting the passivity. One other possible reason is that increased temperature leads to rapid dissolution of active elements (Mg and Al) from S-phase particles (Al₂CuMg), leaving Cu-rich regions on the alloys surfaces that may increase breakdown potentials with temperature [39, 40].(iii)Al 7075 experienced the highest current density followed by Al 2024 and then Al 6061 at all temperatures with the exception of 60°C; Al 2024 exhibited higher corrosion current than Al 7075. Figure 12 reveals how the order of corrosion current density at Tafel region of the studied Al alloys changed at high temperature 60°C compared to low temperature 25°C. Other researchers [17] also found that Al 2024 exhibited higher cathodic current density in chloride solution than Al 7075 and they related this order by the number of cathodic active IM particles. Numbers of catholically active Cu-containing IM particles increased in this order: Al 6061 < Al 7075 < Al 2024. Corrosion current rate of Al 7075 was less influenced by temperature than Al 6061 and Al 2024; Cavanaugh et al. [40] reported nearly the same behavior of MgZn₂ (one of the constituent particles population in Al 7075) with temperature in chloride solution; the electrochemical response of MgZn₂ did not show great variation with temperature from 25°C to 60°C, so we predicted that MgZn₂ particle has a very important effect on the overall behavior of Al 7075.

(a)

(b)

Figure 11: Dependence of (a) and (b) of Al alloys in the Red Sea water on temperature.

Figure 12: Potentiodynamic polarization curves of Al alloys in the Red Sea water at 25°C and 60°C temperature.

3.3. Surface Characterization (SEM and EDS)

Figure 13 depicts SEM images of the studied alloys (Al 7075, Al 2024, and Al 6061, resp.) “A” before and “B” after immersion in the Red Sea water for five weeks. Before taking images, sample A was abraded and treated as referred in Section 2.1 and sample B was pickled in nitric acid to remove corrosion products. SEM images “A” display noncorroded surfaces with scratches due to polishing. Heterogeneous nature of aluminum alloys surfaces is evident by images “A”. SEM images “B” show damaged surfaces due to localized attack by the Red Sea water. Al 6061 is less damaged than other alloys. Pits can be observed in Al 7075 and Al 2024 images. Flakes of corrosion products are shown in Al 7075.

Figure 13: SEM images of Al 7075, Al 2024, and Al 6061 “A” before and “B” after being immersed in the Red Sea water for 5 weeks. The arrows indicate the pits.

For EDS results represented in Figures 14–16, two different samples of the same alloy type were detected by EDS to analyze the elements present on the whole surface (A, noncorroded sample, and B, corroded sample); so, it is thought that EDS analysis lost some degree of precision. In general, Al percent decreased after immersion in seawater and oxygen increased. Copper content in Al 2024 was almost constant before and after corrosion because of the cathodic nature of the copper and Cu-rich particles with respect to alloy matrix. S peak was observed in Al 7075 spectra after corrosion. Appearance of S on Al 7075 after corrosion gives an indication of the contribution of bacteria in corrosion process as SRB. Sulfate reducing bacteria exist in seawater and obtain their energy by reducing sulfate ions to highly corrosive sulfide ions such as , , or S or metal sulfides which can accelerate the electrochemical reaction of corrosion. Previous literature proved that SRB induces pitting corrosion for Al 7075 and Al 2024 [18].

Figure 14: EDS results of Al 7075 “A” before and “B” after being immersed in the Red Sea water for 5 weeks.

Figure 15: EDS results of Al 2024 “A” before and “B” after being immersed in the Red Sea water for 5 weeks.

Figure 16: EDS results of Al 6061 “A” before and “B” after being immersed in the Red Sea water for 5 weeks.

4. Conclusion

The corrosion behavior of Al 7075, Al 2024, and Al 6061 was investigated in this research and the results revealed the following:

(i)The corrosion rates of Al alloys decreased with time and the weight loss data for 32 weeks were consistent with the bimodal model.(ii)Increase in temperature led to an increase in both anodic and cathodic current density and a decrease in corrosion potential. Lowering corrosion potential was associated with an increase in breakdown potential which resulted in expanding the passivity region with temperature(iii)All the alloys suffered from pitting corrosion and the most corroded alloy was Al 7075. Al 6061 showed the highest corrosion resistance at all the immersion times.

Conflicts of Interest

The authors declare that there are no conflicts of interest regarding the publication of this article.

Acknowledgments

The authors are immensely grateful to Professor Robert E. Melchers, University of Newcastle, for his comments on WL data. He agreed with us that the data are consistent with bimodal model and explained the reason for the observation of the bimodal model with short-immersion time as we wrote in kinetic study section.

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