E ﬀ ect of Thermo-Mechanical Processing on the Corrosion Behavior of Fe − 30Mn − 5Al − 0.5C TWIP Steel

: Electrochemical corrosion of thermo-mechanically processed (TMP) and recrystallized Fe − 30Mn − 5Al − 0.5C twinning-induced plasticity (TWIP) steels containing 30 wt.% Mn was studied in a 1.0 wt.% NaCl electrolyte solution. The alkaline nature of the corrosion products containing manganese oxide (MnO) increases the dissolution kinetics of the TWIP steel in acid media, obtaining Mn 2 + cations in solution, and producing the hydrogen evolution reaction (HER). X-ray photoelectron spectroscopy (XPS) surface analysis revealed an increased Al 2 O 3 content of 91% in the passive layer of the recrystallized TWIP steel specimen, while in contrast only a 43% Al 2 O 3 was found on the TMP specimen. Additionally, the chemical composition of the surface oxide layer as well as the TWIP alloy microstructure was analyzed by optical microscopy (OM) and scanning electron microscopy (SEM). The results indicate an enhanced corrosion attack for the TMP high-Mn TWIP steel.

The main alloying element in TWIP steels is considered to be Mn due to its crucial roles in preserving the austenitic structure as well as controlling the stacking fault energy (SFE) of the ternary Fe−Mn−Al alloy [9,10]. Depending on the magnitude of the SFE, different phase transformation processes can be promoted. For instance, martensitic transformation is favored for SFE values below 12 mJ/m 2 ; predominant twinning and gliding dislocation mechanisms are found between 12 and 35 mJ/m 2 ; and above 35 mJ/m 2 dislocation glide is the dominant deformation mechanism [11][12][13].
With superior formability and excellent tensile strength, high-Mn TWIP steel offers improved mechanical properties through strain hardening. Consequently, the use of high-Mn TWIP steel is of paramount important to decrease structural components' weight, while improving the press forming behavior. These benefits are highly sought in the automotive industry for decreasing fuel consumption and reducing greenhouse gas emissions [14,15]. High-Mn TWIP steels (15)(16)(17)(18)(19)(20)(21)(22)(23)(24)(25)(26)(27)(28)(29)(30) wt.% Mn) present a wide range of applications, for instance, structural elements in the automotive industry. This is due to the high tensile strength (above 1 GPa) as well as a great tensile-strength-to-ductility ratio. Furthermore, TWIP steels present higher energy absorption properties (>55 kJ/kg), as compared to other advance high-strength steel (AHSS) grades such as transformation induced plasticity (TRIP) steel TRIP700, and also the dual phase (DP) steel DP600 [16][17][18][19]. Due to their impact resistance, effectiveness, and low environmental impact, TWIP steels have become of major interest in the automotive industry. However, the corrosion of TWIP steels presents a significant hurdle for their practical use [20][21][22].
It has been reported that cold plasticity deformation of high-Mn TWIP steels enhances the susceptibility of corrosion [23][24][25]. Furthermore, the higher Mn content promotes the electrochemical activity of the alloy in chloride and acidic solutions [26]. An increase in the electrochemical dissolution kinetics of TWIP steel has been observed in acid media due to the presence of alkaline Mn oxide (MnO) in the corrosion products. This increased anodic dissolution is attributed to the presence of Mn 2+ cations in solution, and the subsequent hydrogen evolution reaction (HER) on the cathodic half-cell electrochemical reaction [27].
Increased Al content in high-Mn TWIP steel has been shown to improve corrosion performance, while additions of Mn reduce the corrosion resistance [28,29]. Despite the more active standard reversible potential of Al than that of Mn, E Al3+/Al = −1.66 V SHE and E Mn2+/Mn = −1.18 V SHE , respectively, where SHE is standard hydrogen electrode, the higher Mn content governs the anodic dissolution reaction on TWIP steels [30]. Al has been found to impart corrosion protection on TWIP steels by the formation of a stable aluminum oxide (Al 2 O 3 ) passive surface layer [31]. Moreover, Al addition decreases the corrosion current density (i corr ) while increasing the corrosion potential (E corr ) towards nobler values, whereas increased Mn content produces the opposite effect [32]. Lastly, the corrosion resistance was shown experimentally to increase with Al additions and decrease with Mn additions by polarization curves of Fe−Mn−Al alloys in sodium hydroxide (NaOH) solution [26].
This work aims to reveal the influence of the thermo-mechanical process on the corrosion performance of high-Mn TWIP steels. To better understand the correlation between microstructure and corrosion mechanisms, a recrystallized high-Mn TWIP steel was also studied. Electrochemical corrosion behavior was investigated in a 1.0 wt.% NaCl solution and the corrosion products, alloy microstructure and surface composition and morphology were studied by electrochemical methods and surface analysis techniques.

Materials and Methods
The elemental composition of as-cast high-Mn TWIP steel ingots containing 30 wt.% Mn, 5 wt.% Al, 0.5 wt.% C, 0.01 wt.% S, <0.01 wt.% P, and balance Fe, was determined by X-ray fluorescence (XRF) using a S8 Tiger (Bruker, Middleton, WI, USA) wavelength dispersive spectrometer. Specimens were obtained from ingots of TWIP steel prepared in a high temperature furnace using an alumina crucible and argon as a protective gas environment. The main constituents of the alloy are Fe and Mn, while Al and C are the main alloying elements. Figure 1 shows a typical microstructure of as-cast specimens with dendrites and interdendritic spaces of a solidification microstructure.
The ingots were subjected to a thermo-mechanical processing (TMP), which consists of a hot-rolling process at 1100°C. Strips with a final thickness of 2.5 mm were obtained. Subsequently, the strips were subjected to a cold-rolling process to decrease the thickness to 1.5 mm. Followed by recrystallization at 900°C for 30 min, obtaining a microstructure characterized by equiaxial grains of~20 µm in diameter.
For the cyclic potentiodynamic polarization (CPP) test, the specimens were mounted in epoxy resin and the surface was prepared with silicon carbide (SiC) paper, grinding up to 1200 grade, then cleaned with ethanol and deionized water followed by air-drying. Specimens were immediately tested after sample preparation. Furthermore, a protective lacquer was used to prevent crevice corrosion in the resin/alloy interface. The electrolyte used was a deaerated 1 wt.% NaCl solution with 30 min of nitrogen bubbling to avoid oxygen depolarization by oxygen reduction. A 30 min open circuit potential (OCP) monitoring was performed prior to testing until steady-state was reached. Appl. Sci. 2020, 10, x FOR PEER REVIEW 3 of 11 The ingots were subjected to a thermo-mechanical processing (TMP), which consists of a hotrolling process at 1100 ℃. Strips with a final thickness of 2.5 mm were obtained. Subsequently, the strips were subjected to a cold-rolling process to decrease the thickness to 1.5 mm. Followed by recrystallization at 900 ℃ for 30 min, obtaining a microstructure characterized by equiaxial grains of ~20 µm in diameter.
For the cyclic potentiodynamic polarization (CPP) test, the specimens were mounted in epoxy resin and the surface was prepared with silicon carbide (SiC) paper, grinding up to 1200 grade, then cleaned with ethanol and deionized water followed by air-drying. Specimens were immediately tested after sample preparation. Furthermore, a protective lacquer was used to prevent crevice corrosion in the resin/alloy interface. The electrolyte used was a deaerated 1 wt.% NaCl solution with 30 min of nitrogen bubbling to avoid oxygen depolarization by oxygen reduction. A 30 min open circuit potential (OCP) monitoring was performed prior to testing until steady-state was reached.
CPP tests were performed starting from a potential of −0.03 VOCP and scanned anodically until the current density limit of 1.0 × 10 −3 A/cm 2 was achieved, after that, the scan was reversed in the cathodic direction and the scan rate was 0.1667 mV/s according to ASTM G61-86 standard [33]. All experiments were performed at room temperature (~25 ℃ ) and in triplicate, ensuring reproducibility. The polarization tests were performed using a three-electrode electrochemical cell with the TWIP specimen acting as the working electrode, a platinum mesh with a large surface area as the counter electrode, and a saturated calomel (SCE) reference electrode. The CPP tests were performed using a potentiostat/galvanostat Gamry Reference 600 (Gamry Instruments, Warminster, PA, USA).
Specimens for metallographic analysis were prepared by grinding to 2000 grit SiC paper and polishing to a mirror finish using 500 nm non-crystalline colloidal silica. Etching of the polish specimens was done by immersion in Nital solution (10 wt.% HNO3 in ethanol) for 30 s. The microstructure was characterized by optical microscopy (OM) Nikon Eclipse MA 100 (Nikon Metrology Inc., Brighton, MI, USA), scanning electron microscopy (SEM) Hitachi-TM3030 (Hitachi High-Tech America Inc, Schaumburg, IL, USA), and infinite focus microscopy (IFM) in an Alicona infinite focus G5 microscope (Bruker, Itasca, IL, USA).
X-ray photoelectron spectroscopy (XPS) was conducted after a passive layer was generated by potentiostatic polarization for 1 h at −0.750 VSCE in 1.0 wt.% NaCl solution and under deareated conditions. This passive layer formation procedure has been shown in previous works to alter the CPP tests were performed starting from a potential of −0.03 V OCP and scanned anodically until the current density limit of 1.0 × 10 −3 A/cm 2 was achieved, after that, the scan was reversed in the cathodic direction and the scan rate was 0.1667 mV/s according to ASTM G61-86 standard [33]. All experiments were performed at room temperature (~25°C) and in triplicate, ensuring reproducibility. The polarization tests were performed using a three-electrode electrochemical cell with the TWIP specimen acting as the working electrode, a platinum mesh with a large surface area as the counter electrode, and a saturated calomel (SCE) reference electrode. The CPP tests were performed using a potentiostat/galvanostat Gamry Reference 600 (Gamry Instruments, Warminster, PA, USA).
Specimens for metallographic analysis were prepared by grinding to 2000 grit SiC paper and polishing to a mirror finish using 500 nm non-crystalline colloidal silica. Etching of the polish specimens was done by immersion in Nital solution (10 wt.% HNO 3 in ethanol) for 30 s. The microstructure was characterized by optical microscopy (OM) Nikon Eclipse MA 100 (Nikon Metrology Inc., Brighton, MI, USA), scanning electron microscopy (SEM) Hitachi-TM3030 (Hitachi High-Tech America Inc, Schaumburg, IL, USA), and infinite focus microscopy (IFM) in an Alicona infinite focus G5 microscope (Bruker, Itasca, IL, USA).
X-ray photoelectron spectroscopy (XPS) was conducted after a passive layer was generated by potentiostatic polarization for 1 h at −0.750 V SCE in 1.0 wt.% NaCl solution and under deareated conditions. This passive layer formation procedure has been shown in previous works to alter the surface layer [28,34]. In order to minimize surface contamination, the samples were introduced in a nitrogen saturated glove bag to eliminate oxygen contamination immediately after CPP tests.
XPS surface analysis was conducted using a PHI 5000 VersaProbe II (Physical Electronics Inc., Chanhassen, MN, USA) spectrophotometer with an Al K α source (hv = 1486.6 eV), a working residual pressure below 10 −9 torr, a high-voltage excitation of 15 kV, a power of 25 W and a take-off angle of 45 • with respect to the sample surface. The high resolution XPS used a CLAM2 hemispherical electron analyzer with a non-monochromatic Mg K α X-ray source operated at 300 W, with a pass energy of 23.5 eV and at energy step size of 0.2 eV/step. The Fe 2p 3/2 , Al 2p, Mn 2p, O 1s, and C 1s areas were analyzed. The calibration was done on Ag standard substrate, using independent measurements for the Ag 3d 5/2 peak (368.3 eV). A Gaussian-Lorentzian mixed function was used to fit the data, after a Shirley background subtraction [28]. The binding energy reference used was adventitious C, with 285.0 eV for C 1s peak.

Results and Discussion
OM images of TMP and recrystallized TWIP steel samples are presented in Figure 2. Figure 2a shows the TMP specimen microstructure with oriented grains as a consequence of deformation during the hot-rolling process. In contrast, Figure 2b includes the recrystallized TWIP steel specimen showing a homogeneous γ-austenite monophasic microstructure with equiaxial grains and the presence of annealing twin formation on individual grains during recrystallization and grain growth processes. In addition to the annealing twin formation, an increase in the grain size of the recrystallized TWIP samples is seen, similar to what it can be seen in the literature at that temperature range [35,36]. While the recrystallization decreases the dislocation density, the twin density is not affected as much, most of the twins remaining previously formed [35].
analyzer with a non-monochromatic Mg Kα X-ray source operated at 300 W, with a pass energy of 23.5 eV and at energy step size of 0.2 eV/step. The Fe 2p3/2, Al 2p, Mn 2p, O 1s, and C 1s areas were analyzed. The calibration was done on Ag standard substrate, using independent measurements for the Ag 3d5/2 peak (368.3 eV). A Gaussian-Lorentzian mixed function was used to fit the data, after a Shirley background subtraction [28]. The binding energy reference used was adventitious C, with 285.0 eV for C 1s peak.

Results and Discussion
OM images of TMP and recrystallized TWIP steel samples are presented in Figure 2. Figure 2a shows the TMP specimen microstructure with oriented grains as a consequence of deformation during the hot-rolling process. In contrast, Figure 2b includes the recrystallized TWIP steel specimen showing a homogeneous γ-austenite monophasic microstructure with equiaxial grains and the presence of annealing twin formation on individual grains during recrystallization and grain growth processes. In addition to the annealing twin formation, an increase in the grain size of the recrystallized TWIP samples is seen, similar to what it can be seen in the literature at that temperature range [35,36]. While the recrystallization decreases the dislocation density, the twin density is not affected as much, most of the twins remaining previously formed [35]. To further study the microstructure of the recrystallized specimen, SEM micrographs were taken. Figure 3 shows a typical austenitic monophasic microstructure for the recrystallized specimens, confirming the homogeneous γ-austenite monophasic microstructure with equiaxial grains and the presence of annealing twin formation on individual grains. To further study the microstructure of the recrystallized specimen, SEM micrographs were taken. Figure 3 shows a typical austenitic monophasic microstructure for the recrystallized specimens, confirming the homogeneous γ-austenite monophasic microstructure with equiaxial grains and the presence of annealing twin formation on individual grains. CPP curves for TMP and recrystallized TWIP steel specimens immersed in the deaerated 1.0 wt.% NaCl solution at RT are presented in Figure 4 to compare the electrochemical behavior. A passive-like behavior can be observed in both samples. The passive current density (ipass), which indicates the passivity plateau, can be observed with values around 18.03 µA/cm 2 for both the TMP and recrystallized specimens. Furthermore, an increase in the pitting potential (Epit) which is defined by an abrupt increase in the current density, can be observed. It should be noted that in the absence CPP curves for TMP and recrystallized TWIP steel specimens immersed in the deaerated 1.0 wt.% NaCl solution at RT are presented in Figure 4 to compare the electrochemical behavior. A passive-like behavior can be observed in both samples. The passive current density (i pass ), which indicates the passivity plateau, can be observed with values around 18.03 µA/cm 2 for both the TMP and recrystallized specimens. Furthermore, an increase in the pitting potential (E pit ) which is defined by an abrupt increase in the current density, can be observed. It should be noted that in the absence of oxygen in the deaerated 1.0 wt.% NaCl solution, the primary cathodic reaction is HER. If an activation-controlled kinetics is assumed, the behavior can be explained via an increase in the reversible potential for the HER (E rev,H ) due to a pH decrease in the solution as well as an increase in the catalytic properties of the surfaces towards the HER. Differences can be observed between the TMP and recrystallized specimens. The TMP TWIP steel showed higher values for the cathodic current density than the recrystallized specimen. CPP curves for TMP and recrystallized TWIP steel specimens immersed in the deaerated 1.0 wt.% NaCl solution at RT are presented in Figure 4 to compare the electrochemical behavior. A passive-like behavior can be observed in both samples. The passive current density (ipass), which indicates the passivity plateau, can be observed with values around 18.03 µA/cm 2 for both the TMP and recrystallized specimens. Furthermore, an increase in the pitting potential (Epit) which is defined by an abrupt increase in the current density, can be observed. It should be noted that in the absence of oxygen in the deaerated 1.0 wt.% NaCl solution, the primary cathodic reaction is HER. If an activation-controlled kinetics is assumed, the behavior can be explained via an increase in the reversible potential for the HER (Erev,H) due to a pH decrease in the solution as well as an increase in the catalytic properties of the surfaces towards the HER. Differences can be observed between the TMP and recrystallized specimens. The TMP TWIP steel showed higher values for the cathodic current density than the recrystallized specimen.  Differences can also be observed in the anodic kinetics. For the TMP TWIP specimen, a small passivity plateau was drawn with an i pass value of 9.44 µA/cm 2 , this low i pass may be related to the protective properties of the thin and stable Al oxide layer formed. This Al imparts passivity via the formation of an Al 2 O 3 layer [28]. Comparatively, Al displays a more active behavior than Mn, hindering the electrode reaction [28]. It should be noted that Al content not only increases the SFE, but also stabilizes the γ-austenite against phase transformation [6,37]. After reaching the anodic current density limit (1.0 × 10 −3 A/cm 2 ), the polarization was reversed in the cathodic direction in order to assess the repassivation behavior of the high-Mn TWIP steels. This repassivation is reached once the recorded current density intersects the forward scan line, defining the protection potential (E prot ). This behavior was showed in both TWIP steel alloys studied after a positive hysteresis loop was observed. The larger this loop, the higher the resistance to repassivation of the alloy and, thus, greater susceptibility to local corrosion is observed. Table 1 summarizes the values for the E corr , E pit , i pass , E prot , and ∆E = E pit − E prot electrochemical parameters obtained from the CPP curves in Figure 4. More noble E corr values were exhibited by the recrystallized specimens than by the TMP specimens, with a small difference of 0.09 V for the recrystallized specimen. Similarly, more positive E pit values were shown for the recrystallized than for TMP specimens, thus indicating a higher resistance to pitting corrosion, which may be interpreted as a less protective passive layer formed on the TMP specimen than that of the recrystallized specimen. In general, both type of specimens (TMP and recrystallized) exhibited the ability to repassivate. The hysteresis loop (∆E), defined by ∆E = E pit − E prot , allows the evaluation of the susceptibility to localized corrosion [35]. Thus, smaller values of ∆E mean higher resistance to pitting. Though, the differences of ∆E for the TMP and recrystallized specimen were found to be 0.147 and 0.059 V SCE , respectively. Table 1. Electrochemical parameters obtained from the CPP tests of TMP and recrystallized TWIP steels in deaerated 1.0 wt.% NaCl solution (see Figure 4).  Figure 5 shows the IFM images of TMP TWIP steel (see Figure 5a,b) and recrystallized TWIP steel specimens (see Figure 5c,d) both after the CPP test in deaerated 1.0 wt.% NaCl solution. Figure 5a,b reveal a higher pit density for the TMP TWIP steel compared to the recrystallized TWIP steel sample [29]. The recrystallization of the grains of TMP TWIP, seen in Figure 3, decreased the locations for pits to nucleate, as well as the recrystallization made for a greater alumina layer which enhanced the corrosion protection of the samples (see Figure 5c,d). Despite the addition of the recrystallization process, a similar pit depth of~6 µm was found on both specimens, while wider pits were shown on the TMP TWIP specimen, therefore a small pit aspect ratio is depicted for the recrystallized TWIP steel specimen.  The high resolution XPS spectra of the TMP TWIP steel is presented in Figures 6 and 7 for Fe 2p3/2 and Al 2p, respectively. Four peaks were assigned to iron, metallic Fe at 707.2 eV, Fe 2+ oxide (FeO) at 709.2 eV, Fe 3+ oxide (Fe2O3) at 711.2 eV, and Fe 3+ oxyhydroxide (α-, β-or γ-FeOOH) at 713.3 eV as observed in Figure 6 [34,38,39]. Figure 7 shows high resolution XPS spectrum of TMP TWIP steel specimen for Al 2p containing two peaks assigned to metallic Al at 72.0 eV and Al 3+ oxide (Al2O3) at 74.5 eV. This Al2O3 layer present in the surface is related to the passive behavior observed in the CPP tests performed. High resolution XPS spectra for the recrystallized TWIP steel specimen were not included because no additional peaks were revealed, also showing four peaks for Fe 2p3/2, and as observed in Figure 6 [34,38,39]. Figure 7 shows high resolution XPS spectrum of TMP TWIP steel specimen for Al 2p containing two peaks assigned to metallic Al at 72.0 eV and Al 3+ oxide (Al 2 O 3 ) at 74.5 eV. This Al 2 O 3 layer present in the surface is related to the passive behavior observed in the CPP tests performed. High resolution XPS spectra for the recrystallized TWIP steel specimen were not included because no additional peaks were revealed, also showing four peaks for Fe 2p 3/2 , and two peaks for Al 2p. The high resolution XPS spectra of the TMP TWIP steel is presented in Figures 6 and 7 for Fe 2p3/2 and Al 2p, respectively. Four peaks were assigned to iron, metallic Fe at 707.2 eV, Fe 2+ oxide (FeO) at 709.2 eV, Fe 3+ oxide (Fe2O3) at 711.2 eV, and Fe 3+ oxyhydroxide (α-, β-or γ-FeOOH) at 713.3 eV as observed in Figure 6 [34,38,39]. Figure 7 shows high resolution XPS spectrum of TMP TWIP steel specimen for Al 2p containing two peaks assigned to metallic Al at 72.0 eV and Al 3+ oxide (Al2O3) at 74.5 eV. This Al2O3 layer present in the surface is related to the passive behavior observed in the CPP tests performed. High resolution XPS spectra for the recrystallized TWIP steel specimen were not included because no additional peaks were revealed, also showing four peaks for Fe 2p3/2, and two peaks for Al 2p.  A small peak was observed for Mn in both the TMP and recrystallized specimens. Thus, the deconvolution of the data could not be performed. Mn oxides are easily formed and dissolved preferentially at the exposed surface due to the lower stability of the Mn in the Fe−Mn based TWIP steel alloy containing Al [40]. The atomic percentage (at.%) of manganese analyzed was 0.5 and 0.4 at.% Mn for TMP and recrystallized TWIP steel specimens, respectively. A small peak was observed for Mn in both the TMP and recrystallized specimens. Thus, the deconvolution of the data could not be performed. Mn oxides are easily formed and dissolved preferentially at the exposed surface due to the lower stability of the Mn in the Fe−Mn based TWIP steel alloy containing Al [40]. The atomic percentage (at.%) of manganese analyzed was 0.5 and 0.4 at.% Mn for TMP and recrystallized TWIP steel specimens, respectively.
The cationic fractions of Fe cat , Al cat , and Mn cat for Fe, Al, and Mn, respectively, were used to analyze the passive layer composition. The cationic fraction is determined by the relationship between a specific oxide and the addition of each contribution of the oxides that form the passive layer. For instance, the expression for Al would be: Al cat = Al ox /(Fe ox + Al ox + Mn ox ), where Fe ox , Al ox , and Mn ox are the oxides of Fe, Al, and Mn, respectively.
The cationic fractions for Fe, Al, and Mn elements for the TMP specimen were determined to be: 0.43, 0.49, and 0.08 for Al, Fe, and Mn, respectively. For the recrystallized TWIP steel specimen the cationic fractions were: 0.06, 0.91, and 0.03 for Fe, Al, and Mn, respectively. The passive layer of both the TMP and recrystallized TWIP steels is mainly composed of Fe and Al oxides. The content of the Al 2 O 3 in the passive layer increased up to 91% for the recrystallized TWIP, compared with 43% for TMP specimen. As indicated above, the passivating properties of Al alloying element are higher than Fe and Mn [26,31,41]. These results agree with the information supplied by Pourbaix diagram indicating that Al generates a protective and stable Al 2 O 3 layer in the pH range of 4−9 [42]. Therefore, this corroborates the electrochemical CPP results obtained in the present study.
A significant difference in the Gibbs free energy ( G 298 ) at room temperature of the different oxides determines which element will be preferentially oxidized. In this case, the G 298 for the different oxides  [40,43]. Interestingly, despite this enrichment of Al 3+ ions within the oxide layer, other ions were also found in large quantities (Fe 2+ , Fe 3+ , Mn 2+ and Mn 3+ ), indicating that the passive layer should be considered as a mixture of Fe, Al and Mn oxides.

Conclusions
Recrystallized TWIP steel specimens showed homogeneous monophasic austenite microstructure consisting of equiaxial grains with the presence of recrystallization twins. On the TMP TWIP steel specimens, the hot-rolling process generated oriented grains with zones including grain boundary sliding and dislocations glide.
Electrochemical measurements indicated that the TMP TWIP steel presented lower corrosion resistance than the recrystallized specimens. The stability of the passive layer is lower for TMP specimens than for recrystallized specimens, due to the thermo-mechanical processing (TMP) which introduces discontinuities in the alloy matrix. The beneficial effect of Al was also observed on the TWIP steel, promoting a protective passive layer. In general, the hysteresis loop that was defined in the CPP curves decreases for the TMP TWIP steel. Furthermore, an improved corrosion resistance is observed for the recrystallized specimens compared to the TMP TWIP steel.
The pit density decreased with the recrystallization process, as seen from the IFM results, being in good agreement with the CPP analysis. Nevertheless, the pit depth was kept constant at 6 µm for both the TMP and the recrystallized TWIP steel specimens.
XPS analysis for both specimens showed that their passive layers were mainly composed by Fe and Al oxides, metallic Al, and bound water. A small peak of Mn oxide and hydroxide has also been detected.