Influence of Heat Treatment Temperature on the Electrochemical Properties of Cold-Rolled 0.2%C–3%Al–6/8.5%Mn–Fe Medium-Manganese Steel

Abstract

The microstructure evolution, polarization curve and impedance of cold-rolled 0.2%C–3%Al–6/8.5%Mn–Fe steel under heat treatment temperatures of 600–800 °C holding 10 min were tested. The results show that the cold-rolled texture of the steel does not completely disappear at 600 °C and 650 °C, exhibiting high charge transfer resistance R_c and corresponding corrosion potential E_corr. When the heat treatment temperature rises to 700 °C, the texture begins to be eliminated and the R_c begins to decrease, indicating a decrease in corrosion resistance. When the heat treatment temperature rises to 750 °C and 800 °C, it was found that the proportion of austenite begins to increase and the number of grain boundaries decreases, resulting in an increase in R_c and an improvement in the corrosion resistance of the steel. Compared to 6.5 Mn steel, the higher Mn content in 8.5 Mn steel results in better corrosion resistance after high-temperature heat treatment.

1. Introduction

The use of medium-manganese steel in car body manufacturing leads to greater fuel efficiency due to its light weight and excellent mechanical properties. Its dual advantages in cost and performance make it the most promising advanced high-strength steel for the next generation of automobiles [1,2]. In recent years, a large number of scholars have studied the design of medium-manganese steel alloy composition [3], control of rolling process [4] and optimization of heat treatment process [5], achieving a series of important results that have greatly promoted the development of medium-manganese steel [6,7,8]. For instance, Li et al. [9] studied the heat treatment of medium-manganese steel. The results show that the ultimate tensile strength of 1380 MPa and elongation of 39% was obtained after intercritical hardening at 630–650 °C and tempered at 200 °C.

On the other hand, corrosion performance has also become an important consideration in the industrial application of medium-manganese steel [10,11,12]. After production, the car body must undergo anti-corrosion treatment to prevent defects caused by corrosion that could result in a decline in performance. Research has shown that steel is less prone to corrosion when subjected to small deformation, exhibiting strong corrosion resistance. However, as the deformation increases to a large extent, it can lead to a decrease in corrosion resistance [13,14]. Furthermore, studies suggest that the presence of Mn in medium-manganese steel can affect the corrosion rate, which is influenced by other chemical elements. For instance, Su et al. [15] investigated the influence of Mn on the corrosion behavior of medium-manganese steels. The results show that the steels exhibit lower corrosion resistance due to the enrichment of MnFe₂O₄.

However, there are still very few reports on the electrochemical properties of cold-rolled medium-manganese steel, especially the influence of subsequent heat treatment on the electrochemical properties of cold-rolled 0.2%C–3%Al–6/8.5%Mn–Fe. This work discusses the heat treatment of two cold-rolled medium-manganese steels with different Mn contents: 0.2%C–3%Al–6%Mn–Fe (6 Mn) and 0.2%C–3%Al–8.5%Mn–Fe (8.5 Mn). The microstructure evolution of the heat-treated samples was observed. Electrochemical experiments were conducted on the cold-rolled and heat-treated samples to investigate the factors influencing the corrosion performance of medium-manganese steel, providing theoretical guidance for the process design of medium-manganese steel.

2. Materials and Methods

The composition of experimental steels is given in

Table 1. Chemical composition (wt.%) of the two steels.

Steel	C	Al	Mn	Fe
6 Mn	0.20	3.20	6.0	90.60
8.5 Mn	0.19	3.11	8.4	88.30

. The steel ingots were heated at 1200 °C for 2 h in a vacuum induction furnace and then hot-forged into a bar with a cross-sectional size of 100 mm × 30 mm using a Ø450 × 450 two-high reversing hot mill, followed by air-cooling to room temperature. The bar was then soaked at 1200 °C for 2 h followed by 7 passes of hot rolling into a 4 mm-thick strip within a temperature range of 1150–850 °C and air-cooled to room temperature.

After holding the hot-rolled plate at 770–800 °C for 1 h, it was quenched and tempered at 200 °C for 20 min. A 1:3 mixture of hydrochloric acid and water was employed to acid-wash the heat-treated steel plate, followed by cold-rolling using a four-high cold mill with hydraulic tension. After several rolling passes, the thickness was reduced to 1 mm. The cold-rolled samples underwent heat treatment in a furnace, heating to 600 °C, 650 °C, 700 °C, 750 °C, and 800 °C, respectively, were held for 10 min, and then were subjected to water cooling.

The microstructure was analyzed with the help of a field emission scanning electron microscope (SEM) (FEI NOVA NANOSEM 450). To analyze the austenite content in the figures, the percentage of area occupied by austenite was calculated using ImageJ 1.5.4 software [16] to quantify the amount of austenite.

The electrochemical measurements were carried out at room temperature using an electrochemical work station (PARSTAT 2273) with Pt as the counter electrode, saturated calomel electrode as the reference electrode, and the heat-treated samples as the working electrode. For comparative purposes, the as-cold-rolled samples were also tested. A surface area of 1 cm² for each sample was exposed to an electrolyte solution of 3.5% NaCl. The test started by testing the open circuit potential curve with an experimental time set to 3600 s. The impedance spectra were obtained at the open circuit potentials. The frequency range was from 100,000 to 0.01 Hz with a sinusoidal excitation signal of 10 mV. Polarization curves were measured from −1.1 to −0.1 V at a constant rate of potential change of 10 mV·s⁻¹. Subsequently, EIS Spectrum Analyser 1.0 software was used for fitting analysis of the electrochemical impedance spectra curve to obtain a simulated equivalent circuit diagram.

3. Results

3.1. Microstructure Evolution

A type of light-weight medium-manganese steel, 0.2%C–3%Al–6/8.5%Mn–Fe has a dual phase (ferrite and austenite). Figure 1 shows the microstructure of 6 Mn steel after different heat treatment temperatures. It can be observed that after heat treatment at 600 °C and 650 °C, the 6 Mn steel still retains a cold-rolled texture.

As the heat treatment temperature increases to 700 °C and 750 °C, the dual phase of the matrix gradually becomes clearer, with the light-colored protrusions being the austenite phase, appearing in fine stripes, and the dark-colored recesses being the ferrite. The results indicate that with a heat treatment temperature of 700 °C, the austenite area percentage is 32.74%, as shown in Figure 1c. At 750 °C, the austenite area percentage is 43.75% (Figure 1d). At 800 °C, the austenite area percentage is highest, reaching 54.81% (Figure 1e). This is because the heat treatment temperature remains within the two-phase region of the iron–carbon phase diagram. When the temperature reaches 800 °C, the amount of austenite gradually increases, changing from a striped to a granular shape, and begins to grow gradually. This is because of austenite stability increased with increasing temperature [17].

Figure 2 shows the microstructure of 8.5 Mn steel after different heat treatments. It can be observed that 8.5 Mn steel still retains the strip texture from cold-rolling at a heat treatment temperature of 600 °C. As the heat treatment temperature increases to above 650 °C, the texture begins to disappear. At 700 °C, the dual phase gradually appears in the matrix. While the temperature reaches 800 °C, the austenite area percentage is 64.54%. A comparison between Figure 2e and Figure 1e reveals that after heat treatment at 800 °C, the proportion of austenite in 8.5 Mn steel is higher than that in 6 Mn steel.

3.2. Electrochemical Analysis

Polarization curve measurements were conducted on samples of cold-rolled and heat-treated metal, with the experimental results shown in Figure 3. Figure 3a shows the polarization curves of 6 Mn steel at different heat treatment temperatures. Compared to the cold-rolled steel, the passivation zones of all anodic polarization curves after heat treatment have become shorter, indicating the absence of a passivation film on the metal surface. Figure 3b depicts the polarization curves of 8.5 Mn steel at different heat treatment temperatures. By extrapolating the polarization curves, the corrosion current density I_corr, the corresponding corrosion potential E_corr, and the pitting potential E_pit can be obtained, as shown in

Table 2. The polarization curves parameters of 6 Mn steel derived from Figure 3a.

Samples	Ecorr (V) (Mode)	Icorr (A/cm2)	Epit (V) (Mode)
Cold-rolled	−0.82	1.349 × 10−5	−0.44
600 °C	−0.89	1.0 × 10−5	−0.70
650 °C	−0.84	1.288 × 10−5	−0.65
700 °C	−0.86	1.023 × 10−5	−0.70
750 °C	−0.93	3.548 × 10−5	−0.68
800 °C	−0.90	9.120 × 10−6	−0.64

and

Table 3. The polarization curves parameters of 8.5 Mn steel derived from Figure 3b.

Samples	Ecorr (V) (Mode)	Icorr (A/cm2)	Epit (V) (Mode)
Cold-rolled	−0.76	6.025 × 10−6	-
600 °C	−0.92	7.943 × 10−5	−0.49
650 °C	−0.88	1.995 × 10−5	−0.62
700 °C	−0.90	4.786 × 10−5	−0.65
750 °C	−0.89	1.445 × 10−5	−0.65
800 °C	−0.92	2.238 × 10−5	-

.

The parameters from Table 2 and Table 3 indicate that the heat treatment temperature has a certain influence on the E_corr, I_corr, and E_pit. In Table 1, the E_corr of the cold-rolled 6 Mn steel is −0.82 V. After heat treatment, the E_corr of the steel begins to decrease. For example, it decreases to −0.89 V at 600 °C and to the lowest value of −0.93 V at 750 °C. According to electrochemical theory, the more negative E_corr, the greater the material’s corrosion tendency, and the more positive E_corr, the smaller the corrosion tendency. The above results indicate that the increase in heat treatment temperature weakens the corrosion resistance of the medium-manganese steel. In Table 3, compared with the cold-rolled 8.5 Mn steel, the E_corr of the 8.5 Mn steel also shows a decreasing trend overall after heat treatment, but it is not significant.

In Table 2, the I_corr of cold-rolled 6 Mn steel is 1.349 × 10⁻⁵ A/cm². After being subjected to a heat treatment at 600 °C, I_corr begins to decrease to 1.0 × 10⁻⁵ A/cm². Subsequently, with an increase in the heat treatment temperature, I_corr starts to rise, but overall, it shows a gradual decrease. It reaches the lowest value of 9.120 × 10⁻⁶ A/cm² at 800 °C. In Table 3, the I_corr of 8.5 Mn steel also shows an overall decreasing trend, reaching the lowest value of 1.445 × 10⁻⁵ A/cm² at 750 °C. Although the cold-rolled 6/8.5 Mn steel has a smaller tendency to corrode, its I_corr is the highest, resulting in a higher corrosion rate. After heat treatment, it is possible to reduce the corrosion rate, which is beneficial for improving the steel’s corrosion resistance.

Furthermore, observing Table 2, it can be noted that with the increase in heat treatment temperature, the E_pit of 6 Mn steel reaches its lowest value of −0.70 V at 600 °C, and a relatively higher E_pit of −0.64 V at 800 °C. Thermodynamically, this indicates a poorer tendency for pitting at this treatment temperature.

The electrochemical impedance spectroscopy of 0.2%C–3%Al–6/8.5%Mn–Fe medium-manganese steel is shown in Figure 4. It can be observed from the figure that the electrochemical impedance spectra at different heat treatment temperatures all exhibit capacitive arcs. The larger the radius of the capacitive arc, the greater the charge transfer resistance at the metal–solution interface, indicating better corrosion resistance of the metal. With the increase of the heat treatment temperature, the radius of the capacitive arc gradually decreases, reaching the minimum value at 700 °C. When the temperature rises above 750 °C, the radius of the capacitive arc begins to increase again. Therefore, the change trend of the capacitive arc radius indicates that the increase in heat treatment temperature first weakens and then strengthens its corrosion resistance. The corrosion resistance of 6 Mn steel is optimal at 750 °C, while the corrosion resistance of 8.5 Mn steel is optimal at 800 °C.

Figure 5 shows the relationship between the modulus |Z| and frequency (Figure 5a,c), as well as the phase angle and frequency relationship (Figure 5b,d). It can be seen that at high frequencies, the modulus |Z| of 6/8.5 Mn medium-manganese steel is basically the same as that of the heat-treated. In the frequency range of 10⁻² Hz to 10 Hz, there are significant fluctuations. The |Z| of 6 Mn steel is larger when annealed at 750 °C, and in the Bode phase diagram, it has only one maximum phase angle (>50°), indicating relatively good corrosion resistance. Similarly, the |Z| of 8.5 Mn steel is larger when heat-treated at 800 °C, and in the Bode phase diagram, its phase angle also has only one maximum value (>50°).

Using the EIS Spectrum Analyser 1.0 software, the Nyquist plots obtained for all samples in 3.5% NaCl solution were fitted and analyzed. Figure 6 is a simplified model that provides a rough estimate of the corrosion mechanism. The physical meanings of the components in the equivalent circuit diagram are as follows: R_s is the solution resistance, R_c is the charge transfer resistance, and the constant phase element (CPE) represents the double-layer capacitance at the electrode surface. P is the parameter for CPE, and n is the exponent of CPE, with a value range between 0.5 and 1. The magnitude of R_c can be used as a standard to measure the difficulty of electrochemical reactions in the corrosion system, making it a crucial parameter for evaluating the corrosion reaction rate of metals in this corrosion system.

From

Table 4. Fitting parameters acquired from Nyquist diagrams of 6 Mn in Figure 4a.

Samples	Rs (Ω·cm2)	CPE		Rc (Ω·cm2)	% Error
		P (Ω−1·s−n·cm−2)	n
Cold-rolled	7.63	1.09 × 10−3	0.69	760.51	≤4.66
600 °C	6.55	7.58 × 10−4	0.70	521.97	≤3.67
650 °C	9.91	1.58 × 10−3	0.64	433.78	≤4.22
700 °C	8.09	1.20 × 10−3	0.65	338.74	≤7.51
750 °C	7.55	1.52 × 10−3	0.71	1041.10	≤4.31
800 °C	6.17	1.02 × 10−3	0.65	766.51	≤4.44

and

Table 5. Fitting parameters acquired from Nyquist diagrams of 8.5 Mn in Figure 4b.

Samples	Rs (Ω·cm2)	CPE		Rc (Ω·cm2)	% Error
		P (Ω−1·s−n·cm−2)	n
Cold-rolled	6.79	8.13 × 10−4	0.66	730.95	≤2.68
600 °C	8.81	2.38 × 10−3	0.73	974.33	≤7.99
650 °C	9.62	1.31 × 10−3	0.60	772.31	≤6.27
700 °C	7.91	3.42 × 10−3	0.51	436.55	≤5.52
750 °C	7.27	2.34 × 10−3	0.56	813.37	≤4.94
800 °C	9.86	1.13 × 10−3	0.57	1073.41	≤10.31

, it can be seen that the value of index n is between 0.6 and 0.8, indicating that the fitting results of the equivalent circuit are relatively accurate. Deviation from ideality indicates that this electrochemical process is a mixed behavior between ideal resistance and ideal capacitance. As the temperature of heat treatment increases, the value of R_c first decreases and then increases. The value of R_c is much larger than R_s, indicating that the corrosive solution itself has little influence on the electrochemical reaction in the corrosion system, and the corrosion rate is mainly determined by R_c. The R_c value of 6 Mn steel is the highest at a heat treatment temperature of 750 °C, reaching 1041.1 Ω·cm². The R_c value of 8.5 Mn steel is the highest at a heat treatment temperature of 800 °C, reaching 1073.41 Ω·cm². This indicates that at higher heat treatment temperatures, the corrosion resistance of the cold-rolled steel can be improved or restored.

4. Discussion

After cold-rolling, steel will form a texture with a higher ability to resist corrosion and a higher E_corr [18,19,20,21]. After being heat-treated at 600 °C, the texture begins to break down, causing the E_corr to decrease to −0.89 V (6 Mn) and −0.92 V (8.5 Mn). However, these traces of texture are not completely eliminated when annealed at lower temperatures (600 °C and 650 °C), as seen clearly in Figure 1a,b and Figure 2a,b showing the microstructure in a streaked texture state. As the temperature further increases to 700 °C, the texture disappears and its impact on corrosion begins to decrease, causing the E_corr to further decrease and the R_c to decrease as well.

When the influence of texture begins to weaken, the influence of grain size and phase becomes apparent. Due to the higher energy of grain boundaries compared to the matrix, grain boundaries can increase diffusion rates, reduce atomic coordination, enhance electron activity, lower surface work function, and increase R_c, making the surface more prone to electron loss or adsorption [22,23]. This can lead to corrosion at the grain boundaries. At heat treatment of 700 °C, the fine grains of medium-manganese steel result in an excessive number of grain boundaries, and the chemical reactivity of these boundaries starts to be released. This leads to the lowest R_c at this temperature among all the samples (see Table 4 and Table 5), causing the E_corr to decrease and the I_corr to increase, making corrosion easily occur. In Figure 5, both 6 Mn steel and 8.5 Mn steel exhibit the lowest impedance arc radius.

As the heat treatment temperature increases to 750 °C and 800 °C, the material undergoes recovery and recrystallization, causing the grain size to begin increasing and the number of grains to decrease. Previous research results also indicate that with the increase in heat treatment temperature, the grain size of medium-manganese steel begins to increase [24,25], indicating a decrease in the quantity of grain boundaries. A reduced number of grain boundaries is beneficial for the corrosion resistance of the steel. Therefore, at 750 °C and 800 °C, the transfer resistance of 6 Mn and 8.5 Mn steel begins to increase, indicating an improvement in corrosion resistance.

As the temperature of the heat treatment increases, the volume fraction of austenite also begins to increase (see Figure 1 and Figure 2). Research has shown that ferrite is more susceptible to corrosion, while austenite is less prone to corrosion [26,27]. This is also the reason for the continuous increase in the R_c of medium-manganese steel under heat treatment conditions of 750 °C and 800 °C. Due to the increase in austenite content and fewer grains, deformation-induced medium-manganese steel still exhibits good corrosion resistance even in the absence of a textured structure. An increased Mn content contributes to the stability of austenite [28,29]. Furthermore, the increase in Mn also leads to a rise in manganese-containing oxides (such as MnO and Mn₂O₃) [30], thereby improving the density of the passivation film. Therefore, it can be observed that under the same heat treatment conditions, the R_c of 8.5 Mn steel is significantly higher than that of 6 Mn steel.

In summary, it can be seen that due to changes in the microstructure, several influencing factors (mainly phase, texture, and grain boundaries) interact and restrict each other, resulting in varying degrees of changes in the electrochemical performance. At low temperatures, texture plays a major role, while at high temperatures, grain boundaries and phase are important factors in improving the corrosion resistance of medium-manganese steel.

5. Conclusions

This study investigated the electrochemical properties of cold-rolled 6 Mn and 8.5 Mn medium-manganese steels after undergoing heat treatment at different temperatures. With the increase in heat treatment temperature, the E_corr of both steels generally shows a decreasing trend. The trend of R_c initially decreases and then increases. At 700 °C, the R_c of both 6 Mn and 8.5 Mn decrease to the minimum value and then begin to increase again. At a heat treatment temperature of 750 °C, the R_c of 6 Mn steel reaches a maximum of 1041.1 Ω·cm², while 8.5 Mn steel reaches a maximum of 1073.41 Ω·cm² at 800 °C. The change trend is driven by the interplay of texture, phase, and grain boundaries at various stages. Texture plays a significant role during low-temperature heat treatment, leading to a decrease in R_c as it becomes disrupted. In contrast, high-temperature heat treatment eliminates texture entirely, making phase composition the primary factor influencing R_c. Moreover, an increase in the volume fraction of austenite results in a subsequent rise in R_c.