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Article

Microstructure Characteristics and Corrosion Behaviors of Mg-2Zn-2Er-0.3Zr-0.3Mn Alloy under Various Rolling Reductions

by
Yaqi Zheng
,
Yuan Zhang
*,†,
Yun Liu
,
Yaqiang Tian
,
Xiaoping Zheng
and
Liansheng Chen
*,†
Key Laboratory of the Ministry of Education for Modern Metallurgy Technology, College of Metallurgy and Energy, North China University of Science and Technology, Tangshan 063210, China
*
Authors to whom correspondence should be addressed.
†
These authors contributed equally to this work.
Metals 2022, 12(2), 365; https://doi.org/10.3390/met12020365
Submission received: 5 January 2022 / Revised: 11 February 2022 / Accepted: 16 February 2022 / Published: 21 February 2022
(This article belongs to the Section Biobased and Biodegradable Metals)
Browse Figures
Versions Notes

Abstract

:
The poor corrosion resistance of magnesium alloys is one of the major obstacles to their widespread applications in the engineering field and the medical field. A hot deformation process is the main way to improve the corrosion resistance of magnesium alloys. In the present study, X-ray photoelectron spectroscopy (XPS), a scanning electron microscope (SEM), an electron probe micro-analyzer (EPMA) and X-ray diffraction (XRD) were used to investigate the micro-galvanic corrosion behavior and film protection mechanism of hot-rolled Mg-2Zn-2Er-0.3Zr-0.3Mn under 25%, 50% and 75% thickness reductions in Hank’s solution. The results revealed that the best corrosion resistance was obtained in the alloy under a 75% thickness reduction, with a corrosion rate of 0.85 mm/y. The improvement in anti-corrosion was due to the coupling effect of a refined microstructure and dense degradation film on the large deformation hot-rolled alloy. Furthermore, the elements Mn and Er participated in the film formation and stabilized the film structure.

1. Introduction

Mg-based alloys have been regarded as excellent biomedical materials and achieve complete degradation due to a low density, good progressing ability and specific elastic modulus, which is similar to natural bone [1,2]. Nonetheless, in an electrolyte environment with a large number of corrosive ions (Cl−, HPO42−, CO32−, etc.), mechanical integrity may be lost prematurely, even causing tissue necrosis [3,4,5]. A low absolute strength and relatively low corrosion resistance are two main disadvantages that restrict wide industrial and clinical applications of Mg alloys. They are essential to improving the corrosion resistance by alloying elements and performing the deformation process of magnesium alloys for their successful application as bearing structures and implant materials.
The element Er has not been extensively studied to enhance the anti-corrosion ability, while the mechanical property has been significantly improved by using Er [6,7,8,9]. For decades, the corrosion behaviors of Mg-RE-Zn-based alloys containing Mg12YZn, which have long-period stacking-ordered (LPSO) and (Mg, Zn)3Gd phases, have been reported [10,11,12,13,14]. A refined microstructure and compact layers can enhance the corrosion resistance by reducing the micro-galvanic intensity, facilitating the reaction kinetics of film formation and stabilizing the film layer [15,16,17,18,19,20]. Panemangalore et al. [21] found that the corrosion resistance of Mg-2Zn was greatly enhanced by the addition of the element Er (2 wt.%). The corrosion rate decreased from 0.13 to 0.078 mm/y.
Moreover, thermal deformation processes, such as extrusion and rolling, are regarded as effective ways to modify the corrosion resistances of magnesium alloys. Rolling, a significant manufacturing technology for Mg strips or plates, has the advantages of high efficiency and flexibility among all thermal mechanical processes. It can modify the corrosion behavior of Mg alloys by using a refined grain size, reduced segregation and redistributed precipitates. Koleini et al. [22] stated that the hot-rolled process remarkably reduced the high-corrosion tendency of an as-cast Mg-1Ca alloy in an SBF (simulated body fluid) solution. Xiang et al. [23] reported that a current density reduced from 9.5 ± 1.2 × 10−4 to 2.5 ± 2.0 × 10−4 A/cm2 by using the hot-rolled process. Furthermore, Estrin et al. [24] reported that a Mg-4Li-1Ca alloy, processed by using two-step rolling, showed superiority in bone implants. Bakhsheshi-Rad et al. [25] stated that the corrosion resistance is related to the secondary phase. However, corrosion occurs preferentially at the interface between the LPSO phase and the Mg matrix. The 18R-LPSO phase combines well with the matrix and also keeps a high corrosion resistance. Thus, the corrosion resistance of a Mg-Zn-Y-Er alloy can be improved. These opinions provide a new perspective for developing Mg-Zn-Er alloys. Moreover, the elements Er and Mn are considered to be beneficial to the corrosion behavior of Mg alloys [26,27].
Until now, little research has referred to the corrosion behavior of Mg-Er alloys. In this study, a Mg-2Zn-2Er-0.3Mn-0.3Zr (wt.%) (MZEZM) alloy was used to study the influence of hot rolling on the corrosion resistance of MZEZM. Weight loss tests, electrochemical tests and corrosion morphology observations were systematically performed to evaluate the corrosion rate with different processing conditions in Hank’s solution. Finally, the degradation mechanism, by using the synergistic effect of the refined-grain structure and the stability of the corrosion film, was revealed.

2. Materials and Methods

2.1. Materials Fabrication

Mg-2Zn-2Er-0.3Zr-0.3Mn was prepared by using an electric resistance furnace (MRL-8, Huizhou Tianji Magnesium Industry Co., Ltd., Guangdong, China). The alloy elements Zn, Er, Mn and Zr were added by melting pure zinc (99.9% purity), Mg-30Zr (99.9% purity), Mg-10Mn (99.9% purity) and Mg-20Er (99.9% purity) master alloys. To ensure proper alloying, the master alloys were melted at 750 °C for 20 min under a protective gas of N2 and SF6 with a volume ratio of 6:1. Then, the molten alloy was poured into graphite molds with zinc oxide coatings. The as-cast samples were annealed at 350 °C for 12 h and cooled down in air. The total reductions in thickness were 25 (2 steps), 50 (5 steps) and 75% (9 steps), named HR-25, HR-50 and HR-75, respectively. Between each two-rolling step, samples were reheated to 350 °C for 10 min. The deformation of each pass was less than 15%, which was intended to avoid cracking.

2.2. Microstructure Characteristics

Test specimens were mechanically ground on silicon carbide sand paper (#160, #400, #800, #1500, #2500 and #3000) in sequence, then polished and etched with a mixed solution of 4 g picric acid, 3.6 mL glacial acetic acid, 70 mL absolute ethanol and 16.4 mL deionized (DI) water. The corrosion product was removed by using a 200 g/L CrO3 and 10 g/L AgNO3 solution for 60 s and then was weighted with analytical balances. The microstructures were revealed by using optical microscopy (OM, DM6M, Leica, Brackenheim, Germany), a scanning electron microscope (SEM, Scios, FEI Company, Brno, Czech Republic) and an electron probe micro-analyzer (EPMA, JXA-8230, Rigaku Corporation, Yamanashi, Japan), which was equipped with a back-scattered electron imaging mode. Phase analyses were performed with an X-ray diffractometer (XRD, D/MAX2500PC, JEOL, Tokyo, Japan) with CuKα radiation at a scanning speed of 10°/min.

2.3. Weight Loss Test

The samples for electrochemical tests were ground on SiC papers of up to 2500 grit and then washed thoroughly with distilled water and dried by using cold air. For weight loss testing in Hank’s solution, each sample with a cross-section of about 10 mm (RD: rolling direction) × 10 mm (TD: transverse direction) and a thickness of about 1.5 mm was immersed for 7 days at 37 °C. After the immersion test, the corroded specimens were carefully cleaned with a solution consisting of 200 g/L of CrO3 and 10 g/L of AgNO3 at 100 °C, and then the mass changes were measured with a precision balance. The corrosion rate (mm/y) was calculated by using the following equation [28]:
CR = 8.67 × 104 × ΔW/(A·T·D)
where Δw was the weight loss after the immersion test, g; A was the surface area of the samples, cm2; T was the period of the immersion test, hours and D was the density of the sample, g·cm−3.

2.4. Electrochemical Testing

All the electrochemical measurements were performed at an electrochemical work station (CORRTEST CS2350, Wuhan, China) with a conventional three-electrode system in Hank’s solution, incorporated with a saturated calomel electrode (SCE), a Pt counter electrode and a working electrode (testing materials). Electrochemical measurements were conducted on samples with an area of 1 cm2. The samples were immersed in Hank’s solution for 15 min to obtain a relatively stable open-circuit potential (EOCP). Then, the potentiodynamic polarization was set with a scan rate of 1 mV and a scan range from −0.6 V to 0.6 V (relative to EOCP). Three samples were tested for each electrochemical to reduce errors. The Tafel extrapolation method was used to fit polarization curves using the software CView (Version 3.5d, Scribner Associates, Inc., North Carolina, USA ). In Equation (2), the corrosion rate Pi (mm/y) could be calculated by using the corrosion current density, icorr (μA/cm2) [28]:
Pi = 22.85 icorr
Furthermore, the corrosion resistance of the sample was evaluated by using electrochemical impedance spectroscopy (EIS) measurements in Hank’s solution at a body temperature of 37 °C. The EIS measurements were obtained (100 kHz~100 mHz) with an amplitude signal of 5 mV (EOCP). The EIS data were fitted and analyzed by using the software Zsimpwin (Version 3.60, EChem Software, Ann Arbor, Michigan, USA). At least three samples were tested for each composition for the electrochemical measurements to ensure accuracy.

2.5. X-ray Photoelectron Spectroscopy

X-ray photoelectron spectroscopy (XPS, Thermo Scientific EACALAB Xi+, ThermoFisher, Waltham, MA, USA) measurements were performed on the films of corroded MZEZM alloys to analyze the compositions of the corrosion products. The software Avantage (Version 5.948, Micro Focus Ltd., Newbury, UK) was used to fit the XPS data. A C1s peak (284.6 eV) was used to correct the binding energy scale.

3. Results

3.1. Microstructural Characterization

Figure 1 shows the OM microstructures of the as-cast and hot-rolled (HR) samples. For the HR samples, the horizontal direction was the hot-rolled direction. At the deformation of 25%, a large number of lamellar twins appeared in the Mg matrix, accompanied by the phenomenon of a twin–twin intersection in the original grains. The dynamic recrystallization (DRX) nucleation began to occur at the twin–twin intersection (Figure 1b). With the increase in the deformation, the fraction of DRX increased. A large number of equiaxed grains existed in the HR-50 and HR-75 alloys due to the large deformation process. Figure 2 shows EPMA images of the HR-75 alloy, which represent the α-Mg grains, secondary phases and element distributions. An EPMA analysis was carried out in order to further analyze the distributions of the other micro-alloying elements in the alloys. Figure 2 shows the element maps of Mg, Zn and Er. The elements Zn and Er are obviously enriched in the secondary phases, which are located at the grain boundary. During the hot-rolled progress, the secondary phases were broken.
Figure 3 shows the XRD patterns of the Mg-2Zn-2Er-0.3Zr-0.3Mn as-cast and hot-rolled alloys, respectively. In the picture, the diffraction peaks of the W phase (face-centered cubic phase, Mg3Zn3Er2) and α-Mg are observed. A small Mg-Zn binary phase was detected in the as-cast and HR samples. Moreover, with the hot-rolled process, the α-Mg (0002) and (2 1 ¯ 1 ¯ 2) peak of the sample shifted to a higher angle, which indicated that the basal texture increased during the deformation process. A reflection of lattice distortion was caused by macroscopic residual stress.

3.2. Corrosion Behavior of MZEZM Alloy in Hank’s Solution

Weight Loss Test

The weight loss rates of the four samples after immersion in Hank’s solution for 7 days was measured, and the responsible data are listed in Table 1. The weight loss rates of the as-cast and HR-25 samples were larger than those of the other two samples during the immersion test, implying that the as-cast and HR-25 alloys suffered more corrosion damage. It should be mentioned that the corrosion rates of the HR-25, HR-50 and HR-75 alloys decreased in turn by 1.72, 1.08 and 0.85 mm/y, respectively.

3.3. Corrosion Morphologies

3.3.1. The Morphologies and Qualities of Corrosion Products

Figure 4 shows the SEM images of the surface morphologies of the as-cast and hot-rolled alloys after immersion in Hank’s solution for 7 days. The surfaces of all the alloys were covered by accumulated corrosion products. The quantities of corrosion production had increased in the order of HR-25, as-cast, HR-50 and HR-75, suggesting that the HR-75 alloy exhibited the best corrosion resistance. After a 7 day immersion test, a corrosion product layer with a micro-crack covered the surfaces of the HR-75 and HR-50 alloys, while a large number of white precipitation clusters dispersed on the surfaces of the other two samples (Figure 4e). Corrosion products in the shape of needle-like clusters are a typical morphology of brucite [Mg(OH)2] [29], which grows perpendicular to the surface. The XRD data presented in Figure 4g proves that the corrosion products were mainly composed of Mg(OH)2, HA (hydroxyapatite) and MgCO3.

3.3.2. Corrosion Morphology Analysis

After the immersion in Hank’s solution for 7 days, severe localized corrosion was found on the as-cast and HR-25 samples; in contrast, the HR-50 and HR-75 samples revealed uniform corrosion and filiform corrosion. The corrosion films shown in Figure 4a,b reflect that the films were rugged and sparse, which improved the possibility of corrosion ions contacting the substrate. A large number of corrosion pits and gullies, which can be found in Figure 5a,b, improved the ions’ ability to pass through the channel in the sparse corrosion film and produce a strong galvanic corrosion reaction with the substrate. On the contrast, the films of the HR-50 and HR-75 samples were dense and smooth, which was implied by the characteristics of filiform and uniform corrosion (Figure 5c,d).

3.3.3. Polarization Tests

The polarization curves of the as-cast and HR samples after their immersion in an electrolyte for 500 s are shown in Figure 6. The values of corrosion potential (Ecorr) and the corrosion current densities (icorr) extracted from the polarization curves are illustrated in Table 2. The βc represents cathodic slopes. The values of icorr increased with the increase in the rolling reduction. The polarization curves of the as-cast, HR-50 and HR-75 samples had similar characteristics, and a breakdown potential (Ept) appeared near the potential of −1.3 V, which indicated that a temporary protective oxide film was formed on the surface of the sample. A breakdown potential did not exist in the HR-25 alloy. The HR-25 sample had the largest icorr. The corrosion rate decreased in the following order: HR-25 > as-cast > HR-50 > HR-75; it showed the same tendency with the weight loss test.

3.3.4. Electrochemical Impedance Spectroscopy (EIS)

Nyquist curves were plotted from the EIS measurement in Hank’s solution (Figure 7) to further reveal the evolution of degradation behavior during immersion. An equivalent electrical circuit is shown in Figure 7 to fit the EIS data. The EIS of the as-cast, HR-25 and HR-50 samples contained a capacitance loop (high frequency), a capacitance loop (medium frequency) and an inductance loop (low frequency). The inductance loop of HR-75 was small. Rs represented the solution resistance, while the layer resistance (Rf) paralleled with a constant phase element (CPEf), which was related to the oxidized layer. Rct represented the charge transfer resistance related to the dissolution. Moreover, the double layer capacitance in parallel with Rct was represented by CPEdl with the inductance L, which represented the occurrence of a localized corrosion or micro-galvanic event. The comparison of EIS plots proved that there was a better protection ability of the film of HR-75 formed in Hank’s solution than the others.

3.3.5. XPS

To obtain more information about the possible corrosive product, XPS spectra for Mn2p and Er in Hank’s solution were measured and plotted in Figure 8. As displayed in the XRD diffraction in Figure 4g, Mg(OH)2, HA and MgCO3 were enriched in the outer layers of the corrosion products, hinting that the Mg, C, O and P elements precipitated to form the corrosion products during the degradation in Hank’s solution. Nevertheless, according to the XPS survey spectrum in Figure 8, Mn and Er were detected in the corrosion layer. However, the signal of Er4d was low and noisy, confirming the existence of a small amount of the element Er in the corrosion layer.

4. Discussion

According to the electrochemical results, the film morphology and the immersion analysis, there was a significant improvement in the corrosion resistance of the hot-rolled MZEZM alloy with a large deformation. The results showed that the refined microstructure was beneficial for ameliorating the corrosion activity. The percentage of grain boundaries became greater with the smaller grains. Since the activities of the grain boundaries were different from those of the cores, a large number of the grain boundaries could achieve uniform corrosion. Another factor influencing the corrosion activity of the MZEZM alloy was twins. A large amount of deformation twins was observed in the microstructure of HR-25. The deformation twins increased the galvanic corrosion; therefore, HR-25 showed the fastest dissolution rate.

4.1. Microstructure of MZEZM

The as-cast MZEZM had coarser grains with a grain size of about 600 μm, while the HR-50 and HR-75 alloys had more refined grain microstructures of about 8 and 6 μm, approximately 1/75 and 1/100 of the original grain sizes. The HR-25 alloy contained a large number of twins surrounded by small grains. The dynamic recrystallization during the hot-rolled process promoted the grain refinement.
The element Er exhibited a good solubility in Mg at a high temperature. With the decrease in temperature, a Mg3Zn3Er2 phase was observed in the grains and on the boundaries (Figure 2). The element Er also refined the microstructure effectively and reduced the mismatch stress between the α-Mg matrix and the surface, which could decrease the pitting initiation [30]. The controlled addition of Zr and Zn could suppress the adverse effects of the harmful impurities (Fe, Cu, Ni) on corrosion resistance [31,32]. The element Zr could also refine grain size by provide heterogenous nucleation sites. Mn is a common alloying element in Mg alloys because it refines the microstructures of Mg-Zn, Mg-Zn-RE, etc. by using PSN (particle stimulated nucleation). The inhibition effect of the Mn element on the growth of DRX is strong during the elastic deformation process [33]. Moreover, a Mn oxide film acts as a barrier against Cl ion penetration and improves the corrosion properties.

4.2. Comparison of Corrosion Resistances of As-Cast and Hot-Rolled MZEZM Alloys in Hank’s Solution

The corrosion rate values from the immersion in Hank’s solution highlighted the difference between the as-cast and hot-rolled MZEZM alloys (Table 1). The as-cast sample exhibited a larger corrosion rate than the HR-50 and HR-75 samples, while HR-25 showed the highest corrosion rate. Since a large number of twins were produced during the deformation (which can decrease the electrochemical potential of a Mg substrate and increase the anodic dissolution, as shown in Figure 1b), there was a strong micro-galvanic event between the secondary phases and the matrix [34]. After the 7 day immersion test, it was possible to observe small particles, which stacked on the surface (Figure 4b) and were identified as Mg(OH)2 and MgCO3 (Figure 4g) [35,36]. The non-uniform roughened surface showed that the intense hydrogen evolution caused the constant and heterogeneous spalling of the corrosion products from the surface. The intensities of the peaks of corrosion products (Figure 4g), such as Mg(OH)2 and MgCO3, did not follow a certain rule, probably due to the spalling of the oxidation corrosion products. Figure 8 shows that the elements Mn and Er participated in the formation of a corrosion film. Although the element Mn stabilized the film structure [37,38], the severe hydrogen evolution effect had a stronger damage effect on the film layer.
This study confirmed that a large thickness-reduction hot-rolled process can enhance the corrosion resistance of an MZEZM alloy by producing a uniform structure, fine grains and a stable corrosion film. An oxide film can easily form when an MZEZM alloy immerses in Hank’s solution. An active dissolution occurs during the immersion test. Twins and impurities, such as Fe, Ni and Cu, act as cathodes, which are more inter- than anode Mg, thus promoting the micro-galvanic corrosion (reaction (3)–(5)) [39,40]. Then, a porous magnesium hydroxide film is formed on the surface.
2H2O + 2e− → 2OH− + H2↑
Mg → Mg2+ + 2e−
Mg + 2H2O → Mg(OH)2 + H2↑
Figure 6 shows the potentiodynamic polarization measurement of the immersion in Hank’s solution. The corrosion rates from large to small are HR-25, as-cast, HR-50 and HR-75. The current density plateaus on the anodic curves of as-cast, HR-50 and HR-75 were observed and attributed to the protective corrosion film on the surface. On the contrary, the current density of HR-25 increased monotonously. This was consistent with the formation of non-protective properties. This indicated that the twins destroyed the uniformity and integrity of the film. Due to the large deformation, the defects in the matrix were greatly reduced, and HR-75 showed a uniformly corroded surface with the best corrosion resistance.
To further reveal the evolution of corrosion behavior during immersion, Nyquist plots were obtained from the EIS measurement in Hank’s solution (Figure 7). The XRDs of HR-25 and HR-50 indicated larger amounts of corrosion products than HR-75 due to the violent hydrogen-evolution reaction. The reaction produced a loose and porous corrosion film and promoted a continuous reaction between the matrix and corrosion ions. The subsequent reactions produced more corrosion products. The dense and flat corrosion film of HR-75 acted as a physical barrier to slow down local corrosion initiation and expansion. This was consistent with EIS and polarization curves. HR-75 had the largest Rct, which indicated that the refined grains could obtain a corrosion film with a good compactness and integrity. In addition, HR-75 showed a small attendance of pitting corrosion, which corresponded to the unobvious low frequency inductance curves. An inductance loop in the low frequency region could be observed from the other three loops (Figure 7), indicating the breakdown of reaction layers. Table 3 shows that the solution resistances (Rs) of the four samples were approximately same, around 10 Ω·cm2. The charge transfer resistances (Rct) and resistances of the films (Rf) determined the corrosion resistances of the alloys. According to the diameter of the loop and fitting parameters, the degradation rates of the samples were HR-25, as-cast, HR-50 and HR-75, in increasing order. Moreover, a larger diameter of the semicircle in the Nyquist plot represented a more superior corrosion protective property [41]. The HR-75 plot showed a much more superior impedance at any frequency than the other three plots. The almost invisible low frequency inductance loop meant that the corrosion film was relatively complete and prevented the local corrosion [42]. The film resistances of HR-50 and HR-75 were much larger than those of as-cast and HR-25 (Table 3). The comparison of EIS plots proved that the films of as-cast and HR-25 contained weak protection abilities. Moreover, the large Rct of HR-50 and HR-75 indicated that the kinetics of Mg dissolution and hydrogen gas evolution were slower than in the as-cast and HR-25 alloys due to the protection of the uniform and dense films. In addition, HR-75 showed an excellent corrosion resistance compared to the corrosion behaviors of the other hot-rolled alloys (Table 4).

5. Conclusions

In this study, Mg-2Zn-2Er-0.3Zr-0.3Mn alloys were prepared by using as-cast and hot-rolled processes. The microstructure and the corrosion behavior of Mg-2Zn-2Er-0.3Mn-0.3Zr in Hank’s solution were systematically investigated. The HR-75 alloy showed a good corrosion resistance and had an excellent potential in the field of high-corrosion resistant Mg-alloy materials. Some conclusions were obtained:
  • The main phase composition included an α-Mg matrix, a W phase and a Mg-Zn phase. With the increase in the hot-rolled reduction, the degree of dispersion distribution of the secondary phase increased. The main factors influencing the corrosion resistance of Mg-Zn-Er-Mn-Zr were the grain size contribution and the film structure. The better long-term degradation performance of the alloy with a large deformation was due to the different structure of the oxide film and the secondary phase and due to the refined grains. The worst corrosion resistance of HR-25 was due to the generation of twins.
  • According to the results of the electrochemical test, the corrosion rates of the four samples were in the order of HR-25, as-cast, HR-50 and HR-75 with the corrosion rates of 2.88, 1.31, 1.01 and 0.85 mm/y, respectively. The reason for the abnormal corrosion rate of HR-25 was that the non-uniform grain-size distribution enhanced the hydrogen evolution effect, leading to the spalling of the oxidation corrosion products and resulting in the weak corrosion resistance of HR-25.
  • The reasons for the high corrosion resistance of HR-50 and HR-75 were that the fine-grain and homogeneous structure could reduce the hydrogen chemical kinetics, protect the integrity of the film and insulate the contact reaction between the erosive ions and the substrate.

Author Contributions

Formal analysis, Y.Z. (Yaqi Zheng) and Y.Z. (Yuan Zhang); resources, Y.T. and X.Z.; data curation, Y.Z. (Yaqi Zheng) and Y.Z. (Yuan Zhang); writing—original draft preparation, Y.Z. (Yaqi Zheng), Y.Z. (Yuan Zhang), Y.L. and L.C. All authors have read and agreed to the published version of the manuscript.

Funding

This research was funded by the Natural Science Foundation of Hebei Province (E2020209153); Natural Science Foundation—Steel and Iron Foundation of Hebei Province (E2020209124; E2020209127); Fundamental Research Funds for the Provincial Universities of Hebei (JYG2019001); State Key Lab of Advanced Metals and Materials (2020-Z12) and Science and Technology Project of Tangshan (20130205b).

Institutional Review Board Statement

Not applicable.

Informed Consent Statement

Not applicable.

Data Availability Statement

Not applicable.

Conflicts of Interest

The authors declare no conflict of interest.

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Metals 12 00365 g001 550
Figure 1. (a–d) Optical micrographs of as-cast, HR-25, HR-50 and HR-75 samples.
Figure 1. (a–d) Optical micrographs of as-cast, HR-25, HR-50 and HR-75 samples.
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Metals 12 00365 g002a 550Metals 12 00365 g002b 550
Figure 2. EPMA analysis of secondary phase distributions of HR-75 alloy (a) Mg element, (b) Zn element, (c) Er element, (d) Mn element, (e) Zr element and (f) microstructure of the secondary phase.
Figure 2. EPMA analysis of secondary phase distributions of HR-75 alloy (a) Mg element, (b) Zn element, (c) Er element, (d) Mn element, (e) Zr element and (f) microstructure of the secondary phase.
Metals 12 00365 g002aMetals 12 00365 g002b
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Figure 3. XRD pattern of the as-cast and hot-rolled alloys.
Figure 3. XRD pattern of the as-cast and hot-rolled alloys.
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Metals 12 00365 g004a 550Metals 12 00365 g004b 550
Figure 4. (a–d) Surface morphologies of as-cast, HR-25, HR-50 and HR-75 alloys after immersion in Hank’s solution for 7 days, (e) enlarged image of the corrosion film, (f) EDS of the corrosion product and (g) XRD patterns of the films of four alloys.
Figure 4. (a–d) Surface morphologies of as-cast, HR-25, HR-50 and HR-75 alloys after immersion in Hank’s solution for 7 days, (e) enlarged image of the corrosion film, (f) EDS of the corrosion product and (g) XRD patterns of the films of four alloys.
Metals 12 00365 g004aMetals 12 00365 g004b
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Figure 5. Corroded surface morphologies of the (a) as-cast alloy, (b) HR-25 alloy, (c) HR-50 alloy and (d) HR-75 alloy after immersion in Hank’s solution for 7 days.
Figure 5. Corroded surface morphologies of the (a) as-cast alloy, (b) HR-25 alloy, (c) HR-50 alloy and (d) HR-75 alloy after immersion in Hank’s solution for 7 days.
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Figure 6. Polarization tests of the as-cast and HR alloys in Hank’s solution.
Figure 6. Polarization tests of the as-cast and HR alloys in Hank’s solution.
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Figure 7. Nyquist plot and equivalent circuits.
Figure 7. Nyquist plot and equivalent circuits.
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Figure 8. XPS analysis of the corrosion products formed on the HR-75 alloy: (a) Mn2p spectrum (b) and Er4d spectrum.
Figure 8. XPS analysis of the corrosion products formed on the HR-75 alloy: (a) Mn2p spectrum (b) and Er4d spectrum.
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Table
Table 1. Corrosion rates of four samples.
Table 1. Corrosion rates of four samples.
SampleCorrosion Rate (mm y−1)
As-cast1.13
HR-251.72
HR-501.08
HR-750.85
Table
Table 2. Polarization-curve fitting results.
Table 2. Polarization-curve fitting results.
StateEcorr (VSCE)βcicorr (μA/cm2)Corrosion Rate (mm/y)
As-Cast−1.47−2.6457.151.31
HR-25−1.46−2.91125.892.88
HR-50−1.44−3.0244.161.01
HR-75−1.46−3.4037.410.85
Table
Table 3. Fitting results of the EIS spectra.
Table 3. Fitting results of the EIS spectra.
SampleRs (Ω·cm2)CPEf (μΩ−1·cm−2·sn)n1Rct (Ω·cm−2)CPEdl (μΩ−1·cm−2·sn)n2Rf (Ω·cm2)L (H·cm2)
As-cast10.571960.80192.74.780.8944.2737.73
25%9.8027.610.93327.55.850.8848.231.41
50%11.682.670.9260.2844.00.80597.201062
75%10.081.80.98114511850.90401.6-
Table
Table 4. Comparison of corrosion rates of hot-rolled Mg alloys in literature and this work.
Table 4. Comparison of corrosion rates of hot-rolled Mg alloys in literature and this work.
AlloySolutionCorrosion Rate (mm/y)Reference
HR-75Hank’s0.85This work
Mg-1.5Sn-0.5Ca0.35 wt.%NaCl4.31[43]
Mg-1.5Sn-0.5Ca-0.1Ce0.35 wt.%NaCl3.12[43]
AZ310.5 M NaCl10.3[44]
Mg-8Sn-1Al-1Zn0.6 M NaCl19[45]
Mg-2Zn-0.2Mn-0.62NdKokubo0.92[15]
Mg-5Gd3.5 wt.% NaCl0.7[46]
Mg-4Li-1CaSBF12.3[47]
Mg-4LiSBF104[47]
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Zheng, Y.; Zhang, Y.; Liu, Y.; Tian, Y.; Zheng, X.; Chen, L. Microstructure Characteristics and Corrosion Behaviors of Mg-2Zn-2Er-0.3Zr-0.3Mn Alloy under Various Rolling Reductions. Metals 2022, 12, 365. https://doi.org/10.3390/met12020365

AMA Style

Zheng Y, Zhang Y, Liu Y, Tian Y, Zheng X, Chen L. Microstructure Characteristics and Corrosion Behaviors of Mg-2Zn-2Er-0.3Zr-0.3Mn Alloy under Various Rolling Reductions. Metals. 2022; 12(2):365. https://doi.org/10.3390/met12020365

Chicago/Turabian Style

Zheng, Yaqi, Yuan Zhang, Yun Liu, Yaqiang Tian, Xiaoping Zheng, and Liansheng Chen. 2022. "Microstructure Characteristics and Corrosion Behaviors of Mg-2Zn-2Er-0.3Zr-0.3Mn Alloy under Various Rolling Reductions" Metals 12, no. 2: 365. https://doi.org/10.3390/met12020365

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