3.5.1. Immersion Test Results
The changes in 24 h weight loss of H111 hot-rolled AA5754 alloy before heat treatment, and after homogenization and aging is shown in
Figure 9; the corrosion rates after 72 h are given comparatively in
Figure 10. While the alloys corroded after aging showed more weight loss, the alloys corroded before heat treatment exhibited better corrosion behavior. Among the alloys, the least weight loss after 24 h was observed in the alloy that was corroded before heat treatment and this value was 0.69 × 10
−3 mg/dm
2. The highest weight loss was observed in the aged alloy with a value of 1.37 × 10
−3 mg/dm
2. The alloy before heat treatment, which corroded after casting, showed the lowest corrosion rate with a value of 0.39 × 10
−3 mg/(dm
2·day) after 72 h. Calabrese et al. [
46] found that the low sensitivity to pitting corrosion in AA5754 can be attributed to the low content and small size of the precipitates. Additionally, Baqerzadeh Chehreh et al. [
47] noted that the presence of a small fraction of iron in AA5754 contributes to its enhanced corrosion resistance in a NaCl solution compared with pure aluminium. However, it is crucial to note that an excessive amount of the segregated β-phase can increase stress corrosion sensitivity [
48]. Additionally, sensitization following the precipitations of Mg
2Si and β-phase Mg
2Al
3 can induce pitting, intergranular corrosion, and stress corrosion in 5XXX series aluminium alloys [
49]. The presence of sensitization in these alloys has been a subject of study due to its implications for their corrosion resistance [
50].
Post-corrosion XRD patterns of H111 hot-rolled AA5754 alloy before heat treatment, after homogenization, and after aging are given in
Figure 11, respectively. In XRD standard cards, the presence of SiO
2 in the alloys before heat treatment is noteworthy. When looking at alloys in general, high X-ray diffraction (XRD) intensity was observed in the alloy (3260.83) after aging. X-ray diffraction (XRD) intensity in a diffraction pattern is a crucial parameter that provides information about the crystalline structure of a material. The intensity of peaks in an XRD pattern corresponds to the amount of X-rays diffracted by the crystal planes within the material. When all peak intensities and peak locations match perfectly with a reference card, the XRD score of the analysed mineral is 100, indicating a high degree of similarity with the theoretical compound [
51]. Moreover, changes in XRD peak intensity can signify variations in the crystallite size, crystal structure, or lattice parameters of a material. For instance, an increase in mean crystallite size is often accompanied by an increase in XRD peak intensity [
52]. Additionally, high-intensity peaks in XRD patterns at specific planes indicate low interplanar distances and closely packed atoms on those planes [
53]. The texture coefficient, which is calculated based on measured relative intensity in XRD patterns, provides insights into the preferred orientation of crystallites in a material [
54]. Post-corrosion XRD peaks of the alloy before heat treatment (
Figure 11a) are at 19.20°; post-corrosion XRD peaks of the homogenized alloy (
Figure 11b) are at 18.85°; and it was observed that the post-corrosion XRD peaks of the aged alloy (
Figure 11c) started at 17.34°. While the beginning of the XRD peaks of the alloys begins with MgO + Al
2O
3, an Mg
2SiO
4 peak was also observed beginning in the alloy before heat treatment. Post-corrosion XRD peaks were found to be common in the alloys SiO
2, MgO, and MgO + Al
2O
3. While there is extra MgO + Al
2O
3 in the alloy (44.25°) before the heat treatment, Al
2O
3 peaks were common after homogenization (38.20°) and aging (44.66°). XRD peaks of the alloy before heat treatment were at 88.50°; XRD peaks of the homogenized alloy were at 83.15°; and it was observed that the XRD peaks of the aged alloy ended at 84.90°.
Research has shown that the presence and distribution of micro-defects play a role in the structural characteristics of the oxide film formed on aluminum surfaces, affecting the intensity of corrosion attacks [
55]. The formation of an oxide layer primarily composed of Al
2O
3 on aluminum surfaces significantly affects the corrosion behavior of the alloys. This oxide layer can either enhance or adversely influence the pitting corrosion resistance of aluminum alloys [
55]. Oxide layers have been shown to inhibit corrosion by creating stable and compact corrosion products that act as barriers against further corrosion [
56]. Conversely, incomplete oxide films can decrease corrosion resistance, leading to accelerated corrosion rates even with increasing oxide film thickness [
57]. The presence of MgO + Al
2O
3 oxide in aluminum alloys plays a crucial role in influencing corrosion behavior. The composition and characteristics of the oxide layer significantly impact the corrosion resistance of the alloys, with protective oxide layers containing Al
2O
3 + MgO contributing to improved performance and passivity against corrosion. Furthermore, studies have highlighted the importance of the oxide layer composition in enhancing corrosion resistance, with the formation of more protective oxide layers containing Al
2O
3 + MgO contributing to improved performance [
58,
59]. When considering the effect of Mg
2SiO
4 oxide on corrosion in aluminum alloys, it is essential to understand how different oxide layers interact with the environment to either enhance or inhibit corrosion. Research has shown that alloying elements, including magnesium and silicon oxides, can impact the passivity of aluminum alloys by stabilizing oxide layers [
60]. These oxide layers, although thinner with increased alloying element contents, contribute to increased corrosion resistance by forming protective barriers against corrosive agents [
60]. Similarly, the presence of Mg
2Si precipitates in aluminum alloys tends to form protective oxides like SiO
2, MgO, and SiO
2 + MgO, contributing to enhanced corrosion resistance [
61].
Figure 12 shows the SEM micrographs of corroded (immersion corrosion) alloys before heat treatment, and after homogenization and aging.
Table 4 shows the EDX analysis of the second stages with different morphologies (1–9) in
Figure 12a–c. In general, when looking at the SEM micrographs (
Figure 12), it is noteworthy that the pit-shaped/porous structures on the corrosion surfaces proliferate and increase in size. In the alloy that was corroded before the heat treatment (
Figure 12a), polygonal gray-contrast-colored structures are seen in the pit at point 1. These structures are thought to have MgO, SiO
2, and Al
2O
3 phases. At point 2, there is a situation similar to point 1, but this time, a larger rectangular-like structure in the pit attracts attention. This phase is thought to be MgO + Al
2O
3. At point 3, there are small pits in a sediment-like formation. Here, it is assumed that MgO + SiO
2, Al
2O
3, MgO + Al
2O
3, and Mg
2SiO
4 phases are present. It is thought that the peak-like structures remaining in the deep pit at point 4 in the corroded alloy after homogenization (
Figure 12b) are Al
2O
3 and MgO. It is assumed that the phases thought to be present at point 5 at point 4 are also seen here. At this point, pits were seen in a dense arrangement on a foliation-like surface. Point 6 is the richest point in oxygen and it is thought that there are MgO + Al
2O
3, Mg
2SiO
4, and MgO + SiO
2 phases here. The small cylinder-like structures in the deep crater at point 7 in the corroded alloy after aging (
Figure 12c) are thought to be MgO. It is assumed that the rectangular/cylindrical structures covering the pit at point 8 are Al
2O
3 and SiO
2. It is thought that the leaf-shaped structures at point 9 are more pointed and the deposits around it may consist of Al
2O
3, SiO
2, and MgO.
3.5.2. Potentiodynamic Polarization (PD) Tests
Potentiodynamic polarization curves are crucial for determining parameters such as corrosion potential, corrosion current density, and corrosion rate, making them a rapid and effective method for evaluating corrosion behavior [
62]. While
Figure 13 shows the current–voltage curves of the H111 hot-rolled AA5754 alloy before heat treatment, and after homogenization and aging,
Table 5 lists its corrosion data. As seen in
Figure 13 and
Table 5, there is a strong decrease in the corrosion current densities (Icorr) of the alloy before heat treatment compared with other alloys. The alloy that was corroded before heat treatment showed the best corrosion behavior by creating a corrosion potential of 1.04 ± 1.5 V at a current density of −586 ± 0.04 μA/cm
2. However, after aging, the corroded alloy showed the worst corrosion behavior with a corrosion potential of 5.16 ± 3.3 V at a current density of −880 ± 0.01 μA/cm
2.
The intermetallic phases Al
3Mg
2 and Al
6Mn play a significant role in the mechanical properties and corrosion behavior of aluminum alloys. Li [
63] found that Al
3Mg
2 exhibits the active dissolution of both Al and Mg elements at low pH, while selective dissolution occurs at higher pH, affecting the corrosion resistance of AA5000 series alloys. Similarly, Jin [
64] observed that the addition of Mg to Al-Si coatings promoted the formation of Al
3Mg
2, which reduced corrosion resistance. Yao [
65] found that the addition of Mn to Mg-3Al alloys improved corrosion resistance by encapsulating detrimental phases. Lachowicz and Jasionowski [
66] observed a significant influence of the Mg
2Si intermetallic phase on the progression of corrosion. The occurrence of localized corrosion on the surface of a material, specifically around well-formed Chinese script-like precipitates, indicates either the anodic behavior of the Mg
2Si phase or a deterioration of the protective surface layer [
67]. Yasakau et al. [
68] reported that β-(Al
3Mg
2) phases, together with Mg
2Si precipitate, exhibit anodic activity. They also observed that these phases dissolve during corrosion, and the corrosion process is further accelerated by the deterioration of the protective oxide film.
Figure 14 shows SEM micrographs of corroded (potentiodynamic polarization) alloys before heat treatment and after homogenization and aging.
Table 6 shows the EDX analysis of the second stages with different morphologies (1–9) in
Figure 14a–c. In general, when looking at the SEM micrographs, it was observed that the alloys corroded with the formation of more porous areas and cracked oxides after homogenization and aging. The potentiodynamic polarization test and immersion test support each other (See
Figure 10). In the alloy that was corroded before the heat treatment (
Figure 14a), triangular-shaped structures formed within the pitting can be seen at the first point. These structures are thought to have MgO, SiO
2, Mg
2SiO
4, and Al
2O
3 phases. At the second point, there are small round-shaped light-gray contrast-colored structures on the rectangular-shaped structure. The phases here are considered as MgO, SiO
2, and Al
2O
3. It is thought that the spiny structures at point 3 are MgO + SiO
2, Al
2O
3, and MgO. It is thought that the obvious band-shaped precipitation at the fourth point in the corroded alloy after homogenization (
Figure 14b) is MgO, SiO
2, and Mg
2SiO
4. The large structures with light-gray contrast at point 5 are thought to be MgO + SiO
2, Al
2O
3, and Mg
2SiO
4. The crater structure formed at point 6 is thought to be MgO and Al
2O
3. It is thought that the formation of MgO and Al
2O
3 film with branched cracks (
Figure 14c) at the seventh point of the corroded alloy after aging increased corrosion. The light-gray contrast MgO, SiO
2, and Al
2O
3 at point 8 and the crater-like MgO + SiO
2, Al
2O
3, and MgO oxides at point 9 containing branched cracks also increased the corrosion rate. The presence of a thicker oxide covering effectively prevented corrosion, whereas the thinner oxide film vanished and its underlying material experienced corrosion. This corresponds to the breaking of the oxide film and the shedding of second-phase practices on the interfaces [
57]. In
Figure 14c, the distributed pitting formation on the surface of the aged H111 hot-rolled AA5754 alloy after the immersion corrosion test explains the high corrosion rate in the aging heat-treatment condition.
After the corrosion test of the unheat-treated H111 hot-rolled AA5754 alloy, it was observed that MgO, SiO
2, Mg
2SiO
4, and Al
2O
3 oxide films were formed on the surface. The formation of oxide films on Al-Mg alloys, including the AA5754 alloy, is a complex process influenced by factors such as heat treatment, humidity, and the presence of other elements. Lea [
69] and Yoon [
70] both discuss the formation of MgO and Al
2O
3 oxide films on the surface of Al-Mg alloys, with Yoon [
70] specifically noting the formation of MgAl
2O
4 spinel as a secondary oxide. Lea [
69] found that the oxidation of Al-Mg alloys during heat treatment results in the formation of a thin self-healing amorphous film of A1
2O
3, which then transforms into a magnesium-rich surface with an island MgO film. Fernández [
71] further explores the influence of films and the presence of other elements on the oxidation and corrosion of these alloys, offering vital insights into the underlying mechanisms. These studies collectively suggest that the formation of MgO, SiO
2, Mg
2SiO
4, and Al
2O
3 oxide films on the corroded surface of the unheat-treated H111 hot-rolled AA5754 alloy is a result of the complex oxidation process influenced by the alloy composition and environmental conditions. Aluminum alloy, a lightweight metal, is used for real-world applications such as the automotive and aerospace industries, and has many advantages such as good corrosion resistance, good economic benefits in product life, and a high recycling utilization rate [
72]. The use of aluminum alloy fuel tanks for the automotive industry not only reduces the consumption of limited resources but also benefits environmental protection. The application of aluminum alloy parts is in green production, which fits the current international trends in automobile manufacturing [
73]. AA 5754-H22 alloy has become widely used in the ship building and aircraft industries due to its tensile properties, bending behavior, and hardness. It is used due to its high corrosion resistance and its good weldability. AA 5754 alloy is also preferred because of its resistance to sea water and chemicals [
74]. Due to the fact that they have a good combination of strength and formability, in addition to having great corrosion resistance, AA 5xxx series alloys are utilized in automotive applications for the purpose of constructing sections of car physiques and chassis [
75,
76].