Effect of Pre-passivation on the Corrosion Behavior of PH13-8Mo Stainless Steel in Industrial—Marine Atmospheric Environment

The corrosion behavior and mechanism of PH13-8Mo stainless steel with and without nitric acid passivated film were studied through 5 years of outdoor exposure tests in industry-marine atmospheric environments in Qingdao, by means of morphological observation, weight-loss measurement, X-ray photoelectron spectroscopy (XPS) and Scanning Kelvin Probe (SKP). The results showed that the pre-passivation certainly inhibits the corrosion, but exhibits an obvious limitation of protection period for PH13-8Mo stainless steel in industrial-marine atmosphere. Compared with bare PH13-8Mo steel, the number and depth of pitting of pre-passivated steel were reduced, and the average corrosion rate decreased by 14.7%. The reasons of improved corrosion resistance included the higher ratio of Cr/Fe and oxide/hydroxide, and the more positive and homogeneous Kelvin voltage potential for the surface of outdoor exposed pre-passivated steel. Meanwhile, the pre-passivation film on the Cr-depleted regions caused by the Cr-rich precipitated phase was preferentially destructed in the atmosphere with Cl⁻, which decreased the protection period.

Introduction

PH13-8Mo is a martensitic age-strengthened stainless steel with a special grade of steel, which has ultra-high strength and toughness while maintaining good plasticity. Because its outstanding mechanical properties and corrosion resistance, as well as its stable performance in high temperature service environments, it is widely favored in the aviation and traditional energy fields (Friedrich and Schumann, 2001; Li et al., 2017). Typical applications are in aerospace connecting fasteners and aircraft landing gear (Imrie, 1970; Munn and Andersson, 1990; Yue et al., 2009). Due to the wide range of aircraft service and complex corrosive environment, especially in industrial marine atmospheres with industrial pollution, high Cl⁻ concentration (Ghods et al., 2010; Hu et al., 2011; Klapper et al., 2013; Chong and Cheung, 2014) and high humidity characteristics (Carmezim et al., 2005; Zou et al., 2014), resistance of PH13-8Mo stainless steel corrosion is especially important for aircraft life and safety.

There are some studies related to corrosion of stainless steel in atmospheric environment (Lo et al., 2009; Li et al., 2015). The influence of surface treatment of 304L stainless steel on atmospheric corrosion resistance was studied by Wallinder et al. (2003). Button and Simm (1985) revealed the corrosion of 316 stainless steel exposed in different parts for 4 to 30 years. Passivation behavior and surface chemistry of 2507 SDSS in acidified artificial seawater have been investigated by Cui et al. (2017). Above literatures revealed that the difference in the composition of the passivation film had a significant effect on the corrosion resistance of stainless steel in the marine atmosphere. It is well-known that passivation films on stainless steel are mainly composed of Cr and Fe oxides (Goutier et al., 2011; Escrivà-Cerdán et al., 2013) which play an important role in corrosion resistance. The passivation film automatically forms on the surface of the stainless steel under natural conditions, but the corrosion resistance of the film is limited, especially for martensitic stainless steels containing relatively low chromium and nickel. Therefore, in industry, materials or components requiring corrosion resistance are chemically treated to form a passivation film on the surface (Wang et al., 2012).

Previous studies on PH13-8Mo stainless steel focused on heat treatment, precipitation hardening and its hydrogen embrittlement sensitivity (Munn and Andersson, 1990; Guo et al., 2015; Dalmau et al., 2018). However, there are relatively few studies on the corrosion resistance of pre-passivated PH13-8Mo steel, and especially, there is no report on the effect and limitation of protection period of pre-passivation on pitting behavior of PH13-8Mo steel in long term of real harsh natural environment.

The experiment in this study was carried out in Tuandao Cape, Qingdao, which has a typical industrial—marine atmosphere (Yan et al., 2017). PH13-8Mo stainless steel samples with and without inorganic pre-passivated surface were exposed in Tuandao Cape for 5 years, and the corrosion behaviors of the steel were investigated. The composition and electrochemical characteristics of the pre-passivated layer and corrosion products were analyzed by microscopic analysis, XPS analysis and scanning Kelvin probes. The protective properties of pre-passivated layer and the corrosion mechanism of PH13-8Mo stainless steel were discussed, which is important for improving the environmental adaptability of materials and ensuring the flight safety of aircraft. The results provide not only the selection and route of surface treatment but also boundedness of protection period for aerospace martensitic stainless steel in industrial—marine atmospheric environment.

Experimental

Materials Preparation

The experimental PH13-8Mo steel is martensitic precipitation hardening stainless steel with the chemical composition (wt. %) of 0.055C - 0.065Si - 0.046Mn - 12.42Cr - 8.14Ni - 1.14Al - 2.40Mo - 0.023P - 0.020S. PH13-8Mo stainless steel samples were oil quenched after being held at 900°C for 1 h, and kept in air for 1 h, then cold treated at 0°C for 1 h. Finally, the samples were tempered at 510°C for 4 h. The as-prepared samples possessed average yield strength of 1,310 MPa, tensile strength of 1,400 MPa and elongation of 10.8%. The internal microstructure and precipitation phase of the samples were observed by transmission electron microscopy (TEM; FEI TECNAI G20). The TEM samples with diameter of 3 mm were prepared by grinding, polishing and twin-jet electropolishing.

Figure 1 shows the precipitation phase inside the PH13-8Mo steel. It can be seen from Figure 1A that the microstructure of the stainless steel is lath martensite and small amount of residual austenite, and the average width of the laths is about 0.2 μm. These laths contain very high density dislocations, which may be resulted from advancing austenite-martensite boundaries or phase transformation stress (Seetharaman et al., 1981; Kong et al., 2018). A small amount of twins appear inside the matrix shown in Figure 1B. These twins have strict planar boundaries. Further, there are a large number of precipitated phase particles inside the PH13-8Mo steel which was analyzed by TEM, and the results are shown in Figure 2. The precipitated phase is mainly rod-shaped M₂₃C₆ phase with large size and circular NiAl-containing phase.

FIGURE 1

Figure 1. TEM micrographs of PH13-8Mo steel (A) martensitic laths, (B) twins at the grain boundary, (C) residual austenite between martensite laths. M, martensite; RA, residual austenite.

FIGURE 2

Figure 2. Bright field TEM image showing the morphologies and chemical composition of the precipitates (A,B).

Passivation Pretreatment and Field Exposure Experiment

The size of the flat samples of PH13-8Mo steel was 100 mm × 50 mm × 3 mm. Before the pre-passivation treatment, the bare samples were sequentially ground with 2,000 grit SiC abrasive papers, and then degreased by acetone and ethanol. After the surface treatment, the steel was subjected to passivation treatment, and the passivation agent is 30% concentrated nitric acid solution. After immersed in the agent for 60 min at temperature of 25°C, the samples were rinsed with distilled water, and then dried at room temperature and placed in a desiccator for use. After the flat samples were cleaned and dried, the original weight of the flat samples was weighed and recorded using an analytical balance with an accuracy of 0.001 g, and then according to “GB 11112-89 Non-ferrous Metal Atmospheric Corrosion Test Method,” the outdoor exposure test was carried out in Qingdao Tuandao Cape belonging to the industrial marine atmosphere. Four parallel samples were tested in each experiment, and the exposure duration was 5 years. The environment data of exposure field during the test period are shown in Table 1.

TABLE 1

Table 1. Environmental data during the experiment.

Weight Loss Measurement

After 5 years of exposure, the corrosion products of the samples were chemically removed by pickling in the solution (200 mL nitric acid plus deionized water to make 1,000 mL solution) for 60 min at 20°C according to GB/T 16545-2015. The samples were then rinsed with distilled water and dried in air. Then, the samples were weighed to obtain the final weights (W₁). The average corrosion rate after exposure was calculated as follows:

$\begin{array}{l}V=\frac{W_0-W_1}{St}\end{array}$

where V is the corrosion rate (g·m⁻²·a⁻¹), W₀ was the original weight (g), W₁ is the final weight (g), S is the surface area (m²), and t is the exposure time (year).

Corrosion morphologies of the exposed samples with and without passivation pretreatment were observed by scanning electron microscopy (SEM, Quanta 250). The elemental composition of the corrosion products was analyzed using EDS. The measurement of the depths of pits and the corresponding morphology observation after rust removal was carried out via a laser confocal microscope. Furthermore, surface element and valence was determined by XPS (X-ray photoelectron spectroscopy).

XPS

X-ray photoelectron spectroscopy (XPS) was carried out before and after exposure to determine the changes on the surface of the PH13-8Mo. The samples were cleaned ultrasonically in acetone before the measurement. A Thermo ESCALAB 250Xi spectrometer equipped with an Al Kα X-ray was used for the XPS analysis, using an accelerating voltage of 15 kV and a current intensity of 12 mA. In order to eliminate any perturbation (charge effects, surface state, etc.), a compensation of charges (in situ correction) was applied and the positions were corrected in reference to the 1 s spectroscopic state of carbon (hν = 1,486.6 eV). The position of the hydrocarbon C1s peak was assumed to be at 284.6 eV and used as an internal standard to determine the binding energy of other photoelectron peaks. The curve fittings were performed with the software Avantage containing JCPDS files database, which contains the Shirley background subtraction and Gaussian–Lorentzian tail function for better spectra fitting.

Scanning Kelvin Probe (SKP)

The Kelvin potential distribution of bare and pre-passivated samples after outdoor exposure was further studied by scanning Kelvin probe. The development of local corrosion can be further studied from the surface potential distribution. The surface Volta potentials were measured by a M370 micro-area scanning electrochemical workstation SKP instrument. The scanning area was 1 mm × 1 mm, and the amplitude was 50 μm. The probe was a tungsten filament, and the working distance of the probe to the surface of the sample was 100 ± 3 μm. The test temperature is controlled at an ambient (25°C), relative humidity is 50%.

The principle of Scanning Kelvin Probe is to detect the electron work function [surface work function ϕ_M, Equation (1)] of the metal surface. The basic properties of the metal itself are defined as the negative value of the actual potential ae of the metal inside the metal, and ϕM is equal to the minimum work done to get the electron out of its Fermi level and transfer it to a point outside the metal surface (e.g., in the air), so it consists of two parts: the chemical potential of electron μe and the potential drop XM across the metal/air section. If the metal surface has a rust layer or a coating, it will increase the voltage to be applied by the excited electrons, causing the surface Kelvin potential to drop. As to PH13-8Mo stainless steel, the electron escapes through a plurality of interfaces from the substrate-passivation film-corrosion product layer-air. The actually measured electron emission work is shown in Equation (2), where β1, β2, β3, q1, q2, q3, and C1, C2, C3 is the potential drops, charges, and capacitances of the three interfaces, respectively (Merl et al., 2004). The relationship between the electronic properties of the passivation film and the pitting potential can be found in the literature (Nazarov and Thierry, 2007).

$\begin{array}{ll}{\Phi }_M=-a_e=-{\mu }_e+e{X}_M& (1)\end{array}$

$\begin{array}{ll}\frac{{\Phi }_{\text{EXP}}}{e}=\frac{{\Phi }_M}{e}+{\beta }_1+{\beta }_2+{\beta }_3=\frac{{\Phi }_M}{e}+\frac{q_1}{C_1}+\frac{q_2}{C_2}+\frac{q_3}{C_3}& (2)\end{array}$

In order to further characterize the surface Kelvin potential distribution of the samples, Gaussian fitting analysis is performed on the test results; the fitting formula is:

$\begin{array}{ll}y=y_0+\frac{A}{\sigma \sqrt{2\pi }}exp\left(-\frac{{(x-\mu )}^2}{2{\sigma }^2}\right)& (3)\end{array}$

Where μ is the expected value, i.e., the focus position of the potential distribution; σ is the standard deviation of the distribution of the Gaussian analysis (i.e., the representative dispersion of the potential distribution; the larger the value, the larger the dispersion potential distribution) (Wang et al., 2019).

Results and Discussion

Weight Loss and Corrosion Rate

The corrosion rates of bare and pre-passivated treatment of PH13-8Mo stainless steel after exposure in Qingdao were 4.07 g·m⁻²·a⁻¹and 3.47 g·m⁻²·a⁻¹, respectively. It can be obviously seen that the corrosion resistance of PH13-8Mo stainless steel was well. Compared with the bare samples, the average corrosion rate of the pre-passivated samples after 5 years exposure test decreased by 14.7%. The corrosion resistance of the PH13-8Mo stainless steel pre-passivated with concentrated nitric acid was stronger than that of the bare steel, the pre-passivation film has a certain protective effect on the PH13-8Mo stainless steel matrix in the industrial marine atmosphere.

Surface Morphologies and Corrosion Product Analysis

Figure 3 shows the macroscopic morphology of exposed PH13-8Mo stainless steel sheets of bare and pre-passivated samples exposed for 1 and 5 years before and after rust removal. For the 1 year exposure samples, both bare and pre-passivated samples depicted significant pitting characteristics, and most areas of the bare sample surface were covered with corrosion products, while the corroded area of the pre-passivated sample was far less, and the metallic luster was visible in local positions. After the 5 year exposure, the overall area of the bare samples lost the silver-white metallic luster, and were covered by the reddish brown corrosion products. In addition, the thickness of the rust layer was uneven as some rust layer fell off, and small dots and flakes were distributed on some locations. As for the pre-passivated sample, the surface was also completely covered by the rust layer, and the macroscopic morphology was almost the same as the bare sample. Specially, the rust layer was mainly distributed on the edge of the samples, which led to the accumulation of thin electrolyte film at the edge and thus induced the more severe corrosion. After rust removal, large amounts of pits were observed on both bare and pre-passivated samples, while the number of pits on the pre-passivated was less and the corresponding sizes were smaller, which indicated the pre-passivation effectively weakened the pitting of the steels. Overall, in the long-term industrial-marine atmospheric environment, the pre-passivation treatment limitedly delayed the occurrence of the pitting and uniform corrosion, but did not alter the corrosion mechanism of the steels.

FIGURE 3

Figure 3. Macroscopic corrosion morphology of each sample (A1–A3) Bare samples exposure for 1 year, exposure for 5 years, and after rust removal of 5 years. (B1–B3) pre-passivated samples exposure for 1 year, exposure for 5 years, and after rust removal of 5 years exposure.

The microscopic morphologies of the exposed stainless steel plate and the chemical compositions of the rust layer and pits were shown in Figure 9. After 5 year exposure, the surface of bare sample was covered by lots of corrosion products which were irregularly deposited in local areas. In addition, the surface of the bare sample exhibited typical pitting characteristics, and the diameters of the pits varied from several micrometers to about 20 μm. While for the pre-passivated samples, there were fewer corrosion products covering the surface of the sample, and the number of the pits significantly decreased. Furthermore, the diameters of the pits measured were within 10 μm, which indicated that the pre-passivation was unable to change the corrosion types, but it greatly inhibited the initiation and propagation of the uniform and pitting corrosion.

It was well-acknowledged that the surface active sites such as inclusions, precipitates and the weak passive film region, were generally assigned as the pitting nucleation locations (Vignal et al., 2014). In PH13-8Mo stainless steel, there were a large amount of Cr-rich M₂₃C₆ precipitates, which induced the emergence of the Cr-depleted zones around the precipitates (Luo et al., 2018), as shown in Figure 2. The surface passive film over the Cr-depleted regions was known to be weak and thus led to the preferential attack (Ryan et al., 2002; Bonagani et al., 2018) by the high concentration of the chloride ion in the industrial-marine atmosphere, which created a priority for the pitting nucleation. Therefore, both the chloride-containing environment and the Cr-rich precipitates played an important role in the initiation of the pitting corrosion. As the exposure time increased, autocatalytic reaction of occlusion cell in the pits and the penetration of the corrosive medium caused the corrosion inside the pits to propagate. From Figure 4, in both bare and pre-passivated stainless steel, the surface corrosion products were mainly composed of Fe, O, Si, Cr, Ni, Mo, while Mo element was not detected in the pitting corrosion products. Mo element had the lower diffusion rate than those of Cr and Ni elements (Jin and Atrens, 1988) that led to the difference of the surface and pitting corrosion products in Figure 4.

FIGURE 4

Figure 4. The microscopic morphologies and EDS analysis of the (A) Bare sample; (B) Pre-passivated sample after 5 years exposure.

Figure 5 showed the surface morphologies of the samples after rust removal and the corresponding depths of the pits. As shown in Figure 5A, the pits on the surface of the bare sample were large and connected into pieces, which tended to be denuded, and the depths could be as deep as 50 μm. While, after pre-passivation treatment, the area and depth of pits significantly decreased compared with the bare sample, and the surface was also relatively flat, which also supported the view that the pre-passivated treatment weakened the propagation of the uniform and pitting corrosion but could not ultimately prevent the occurrence of the corrosion.

FIGURE 5

Figure 5. Microscopic morphologies and the corresponding pit depth of (A) Bare sample; (B) Pre-passivated sample after the rust removal.

The XPS Analysis

The main compositions of the surface of PH13-8Mo stainless steel before and after 5 year exposure were determined by XPS. The XPS survey spectrums of the bare and pre-passivated samples are shown in Figure 6. The high-resolution images of Cr 2p_3/2, Fe 2p_3/2, Mo 3d, and O1s were presented in Figures 7–10, and Table 2 listed the corresponding binding energies of the obtained deconvolution from XPS spectra. As shown in Figure 7A, the Fe 2p_3/2 spectra of the bare samples could be deconvoluted into several peaks representing the metallic state Fe_(met) (706.55 eV), the bivalent (Fe²⁺) and trivalent (Fe³⁺) species. From the Figure 7B1, the relative peak heights of Fe₃O₄ (707.5 eV) and Fe₂O₃ (712.1 eV) indicate that Fe₃O₄ and Fe₂O₃ were the primary iron oxidized species in the passive film before exposure. However, after 5 years of exposure, the surface of the bare sample and the pre-passivated sample were covered with corrosion products, and the composition of the Fe compound was not different. The relative peak heights of Fe₃O₄ (707.34 eV), FeO (709.11 eV), Fe₂O₃ (710.96 eV), FeOOH (712.70 eV) indicated that the corrosion products on the surface of the samples were iron oxide and oxyhydroxide. The anodic process was characterized by the dissolution of iron (Chen et al., 2009):

$\begin{array}{r}\text{Fe}-2{\text{e}}^{-}\to {\text{Fe}}^{2+},\\ {\text{Fe}}^{2+}+2{\text{OH}}^{-}\to {\text{Fe}(\text{OH})}_2\end{array}$

Fe(OH)₂ would be oxidized to FeOOH and Fe₃O₄, while FeOOH was unstable and would continue to be oxidized, the reactions were as follow (Hu et al., 2011):

$\begin{array}{r}4{\text{Fe}(\text{OH})}_2+{\text{O}}_2\to 4\text{FeOOH}+2{\text{H}}_{2}O\\ 2\text{FeOOH}\to {\text{Fe}}_2{\text{O}}_3+3{\text{H}}_{2}O\\ 6{\text{Fe}(\text{OH})}_2+{\text{O}}_2\to 2{\text{Fe}}_3{\text{O}}_4+6{\text{H}}_{2}O\end{array}$

The fitting results of the Cr 2p revealed that there exist four peaks representing metallic state Cr_(met) (573.94 eV), Cr₂O₃ (576.62 eV), CrO₃ (577.93 eV), Cr(OH)₃ (587.18 eV). The intensities of the Cr(OH)₃ and Cr₂O₃ states are apparently higher than that of the Cr(met) and these oxidized components were the primary components of the passive film in stainless steel (Luo et al., 2011). Compared with the bare sample, Cr⁶⁺ was detected in the passive film, which might be introduced via the pre-passivation process (Cheng et al., 2009). The ratio of Cr₂O₃ and Cr(OH)₃ decreased after 5 years exposure, but the content of CrO₃ was relatively stable. In addition, a relatively low intensity Mo 3d spectra was recorded because of the oxidation states of the Mo 3d region overlap, the curve fitting becomes complicated to achieve the spectra owing to the almost similar energy levels of Mo 3d_3/2 and Mo 3d_5/2. The signal intensity of Mo⁴⁺ (228.40 eV, 231.40 eV) increased, which indicated that the pre-passivation enhanced the enrichment of Mo and further made the passive film much denser (Kraack et al., 1995; Rodriguez et al., 2018). The addition of Mo into stainless steel has a significant effect on promoting the enrichment of Cr in the passive film and thus prolonged the induction period in Cl⁻ concentrated environment (Sugimoto and Sawada, 1977; Li et al., 2017).

FIGURE 6

Figure 6. XPS survey spectrum of PH13-8Mo stainless steel: (A1,B1) Bare and pre-passivated sample before exposure; (A2,B2) Bare and pre-passivated sample after 5 year exposure.

FIGURE 7

Figure 7. Experimental and fitted narrow XPS spectra of Fe 2p_3/2 of the surface film of (A1,B1) Bare and pre-passivated sample before exposure; (A2,B2) Bare and pre-passivated sample after 5 year exposure.

FIGURE 8

Figure 8. Experimental and fitted narrow XPS spectra of Cr 2p of the surface film of (A1,B1) Bare and pre-passivated sample before exposure; (A2,B2) Bare and pre-passivated sample after 5 year exposure.

FIGURE 9

Figure 9. Experimental and fitted narrow XPS spectra of Mo 3d of the surface film of (A1,B1) Bare and pre-passivated sample before exposure; (A2,B2) Bare and pre-passivated sample after 5 year exposure.

FIGURE 10

Figure 10. The XPS spectra of O 1s of the passive films formed on PH13-8Mo stainless steel surface (A1,B1) Bare and pre-passivated sample before exposure; (A2,B2) Bare and pre-passivated sample after 5 year exposure.

TABLE 2

Table 2. The binding energies of the primary compounds of the PH13-8Mo stainless steel passive film and corrosion products obtained from XPS spectra deconvolution.

For the pre-passivated samples, the Fe 2p_3/2 spectra could also be separated into three constituent peaks representing the metallic state Fe_(met) (706.61 eV), the bivalent (Fe²⁺) and trivalent (Fe³⁺) species, and the relative peak heights of Fe₃O₄ (707.90 eV), FeO (709.80 eV), Fe₂O₃ (711.50 eV), FeOOH (713.70 eV) were a little different from the bare sample. The intensities of iron oxide and oxhydroxide were lower, which attributed to the fewer corrosion products on the surface than those of the bare sample. For the Cr 2p spectra, there exist six constituent peaks representing metallic state Cr_(met) (574.20 eV), Cr₂O₃ (576.70 eV), Cr(OH)₃ (577.40 eV), and CrO₃ (578.30 eV). In addition, the concentration of the Cr(OH)₃ became less, while the content of Cr₂O₃ increased. Meanwhile, a difference was also displayed in the Mo 3d spectrum, however, the Mo and Mo oxidized species were little difference after exposure.

The oxygen species in the passive film acted as connecting metal ions, which were mainly O²⁻, OH⁻. Figure 10 showed the core-level spectra of the surface film formed on the bare and pre-passivation samples in the O 1s region. The O 1s spectra could be divided into three components, O²⁻ (529.73 eV), OH⁻ (531.22 eV) and H₂O (532.93 eV) in the bare sample, and O²⁻, OH⁻ and H₂O in the pre-passivation sample. Furthermore, it could be seen that O²⁻ was the primary constituent of the passive film and corrosion products, which corresponded to the formation of Cr₂O₃, Fe₂O₃, FeO, and MoO₂. While the OH⁻ was also the primary constituent which corresponded to the formation of Cr(OH)₃ and FeOOH. The fraction of Cr, Fe oxides and hydroxides and the Cr/Fe ratio (at. %) in the passive films of the both samples were listed in Table 3. The concentration of the Fe(met) and Cr(met) decreased sharply after 5 year exposure, which also illustrated that the surface suffered from corrosion and the surface was covered with corrosion products. Previous studies have illustrated that the presence of hydroxides in passive films was detrimental to localized corrosion resistance (Clayton and Lu, 1986). In this work, it could be found that the pre-passivated sample contained more oxides and less hydroxide than that of the bare sample, which reflected that the pre-passivation treatment decreased the fraction of the hydroxide in the passive film and thus enhanced the pitting resistance of the PH13-8Mo stainless steel.

TABLE 3

Table 3. The fraction of Cr and Fe in the surface of the PH13-8 Mo stainless steel.

In addition, a large number of researches reported that the repassivition of stainless steel was mainly due to the maintenance of a certain Cr/Fe ratio (at %) in its passivation film (Ryan et al., 2002; Phadnis et al., 2003, Devaux et al., 1994), and the enrichment of Cr enhanced the stability and corrosion resistance of the passivation film, which resulted in a lower passive current density (Lv et al., 2016). Therefore, it could be found that the Cr/Fe ratio of the bare sample was ~3.54, while it was 4.16 of the pre-passivated sample, which indicated that the pre-passivated treatment could significantly increase the Cr/Fe ratio of the passive film on the PH13-8Mo stainless steel, and thus enhanced the repassivition to protect the propagation of the pitting corrosion. However, after 5 years of outdoor exposure, the difference in the ratio of Cr and Fe on the surface of the bare and the pre-passivated samples was much small, which also manifested that the pre-passivation treatment did have the protectiveness on the stainless steel, but the effect after long-term exposure revealed obvious boundedness of protection period.

SKP

To further study the protective effect of the pre-passivated film of the PH13-8Mo stainless steel, the surface Kelvin potential of the both samples after 5 year exposure was measured. The potential distribution was shown in Figure 11, and the surface potential E_kp was fitted by a Gaussian equation, as shown in Figure 12. The chemical potential of electron μ_e of the bare and the pre-passivation sample was −0.1554 and 0.0377 V, respectively.

FIGURE 11

Figure 11. Surface Kelvin potential distribution after 5 year exposure (A) bare sample; (B) pre-passivated sample.

FIGURE 12

Figure 12. Histogram and fitting curve of Kelvin potential distribution on the surface of PH13-8Mo stainless steel after exposure for 5 years (A) bare samples; (B) pre-passivated samples.

It is found that the potential distribution uniformity between the bare sample and the pre-passivated sample surface is not much different. The value of σ of the bare and the pre-passivation sample was 0.0394 and 0.0383, respectively. The potential difference was obvious between the different regions on the surface, which could be characterized as the localized corrosion. While, the potential distribution of the pre-passivation sample was more even, and the corresponding value of σ was smaller. In addition, the Kelvin potential of the bare sample was much lower than that of the pre-passivated sample according to the Gaussian fitting results.

It was widely accepted that the dense passivation film was a semiconductor film, which strongly inhibited the escape of electrons (Wu et al., 2017) and thus resulted in an increase in the surface Kelvin potential of the stainless steel. (Szklarska-Smialowska, 2002) believed that the breakdown of the passivation film by the electrons was one of the reasons for the initiation of pitting corrosion. Therefore, the higher Kelvin potential of the pre-passivated sample reflected that it was more difficult for the electrons to pass through the pre-passivation film, that was, the passivation film was much denser than that of the bare sample. Herein, combined with Figures 9, 10, the surface of the pre-passivated sample was covered with fewer corrosion products and the denser passivation film, and thus led to more positive surface Kelvin potential.

Conclusions

(1) The 5 year field exposure tests in industrial—marine atmospheric environment showed that, compared with bare steel, pre-passivation treatment inhibited the uniform and pitting corrosion of PH13-8Mo stainless steel, that is, the area and depth of pitting are obviously reduced, and the average corrosion rates of the pre-passivated steels decreased by 14.7%.

(2) Compared with the bare PH13-8Mo stainless steel, the higher ratio of Cr/Fe and oxide/hydroxide, and the more positive and homogeneous Kelvin voltage potential for the surface of outdoor exposed pre-passivated steel inhibited the uniform and pitting corrosion.

(3) The pre-passivated PH13-8Mo stainless steel occurred pitting only after 1 year of exposure. The main reason is that the chromium-depleted passivation film near the Cr-rich precipitates is weak to prevent Cl⁻ permeation and the pitting initiation and propagation, which led to a negative effect for the protection period of pre-passivation.

Data Availability Statement

All datasets generated for this study are included in the article/supplementary material.

Author Contributions

YH and YL conceived and designed the experiments. YL, QZ, and JZ performed the experiments. YL, XC, and LL analyzed the data. YH and JZ contributed reagents, materials, and analysis tools. YL wrote the paper.

Funding

The authors wish to acknowledge the financial support of the National Key Research and Development Program of China (No. 2016YFB0300604), the National Natural Science Foundation of China (Nos. 51971033, 51801011), and the National Materials Corrosion and Protection Data Center.

Conflict of Interest

The authors declare that the research was conducted in the absence of any commercial or financial relationships that could be construed as a potential conflict of interest.

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