Self-Healing Properties of Cerium-Modiﬁed Molybdate Conversion Coating on Steel

: Environmentally friendly alternatives to chromium—phosphate/molybdate and cerium-modiﬁed phosphate/molybdate conversion coatings—were deposited on a carbon steel surface. Different surface analytic techniques were applied to obtain complementary information on the composition, element distribution morphology and inner structure of the coatings in order to establish the relationship between coating properties and corrosion performance. The higher protective and stronger self-healing abilities were found for phosphate/molybdate/cerium conversion coating deposited in a sulphate-containing solution. The protective barrier strength was found to be related with certain aspects of the coating morphology such like homogeneous distribution of ﬁne crystallites and, hence, lower number of structural defects. The self-healing ability depended on both, the composition (higher amount of Ce(IV)) and micro-structural characteristics, such as defectiveness, of the conversion layer.


Introduction
Steel is the most frequently used metal in various industries; however, its susceptibility to corrosion in many environments limits its application. Therefore, a wide variety of coating processes have been developed to achieve coatings with desirable properties to meet certain surface protection requirements. Chromate conversion coatings have been widely applied for corrosion protection of metals, as providing both, barrier and self-healing effects. However, legislative pressure regarding prohibition of Cr(VI) compounds pushed scientists to look for suitable alternatives. Significant efforts have been invested to develop environmentally friendly technologies, including the ones based on phosphates [1][2][3][4], molybdates [5][6][7][8][9] and rare earth (cerium) based chemistries [10][11][12][13][14]. However, only few of them have been able to come close or meet the corrosion protection requirements.
Phosphating is one of the most widely used passivation treatments for steel. Formation of this conversion coating occurs via the growth and coalescence of phosphate crystals, what inevitably leaves pores, which are detrimental for the metal corrosion resistance. The protective ability of phosphate coatings on steel could be improved by the passive layer modification with Mo compounds [6,15]. Molybdates are considered to promote the passive state on the surface of steel, which reduces the passivation current through formation of a stable film and extends the anodic passivation range [8].
Moreover, an active self-healing of defects is required for the total or partial repair of coated areas damaged by ageing or unexpected aggressive events. However, due to the fact that molybdates are weaker oxidizing agents than chromates the resulting coating does not demonstrate a sufficient capacity of self-repair. This ability can be achieved or increased by introduction of specific corrosion inhibitors into the coating system. Rare earth

Sample Preparation
Carbon steel specimens (10 mm × 20 mm × 1 mm) previously polished with emery paper up to grade 400 with polishing equipment Tegramin-25 (Struers, Ballerup, Denmark), degreased with ethanol and rinsed with distilled water, were used as the base metal electrodes. Phosphate-molybdate (Fe/P-Mo) and phosphate-molybdate-cerium (Fe/P-Mo-Ce) coatings were deposited on steel surface. The solution used for the Fe/P-Mo chemical conversion treatment contained: 0. 15  All electrolytes were prepared from analytical grade chemicals and deionized water. In order to create an artificial defect and to evaluate the self-healing ability of the investigated conversion coatings the deposited samples were manually scratched with metallic needle (the width of scratch~30 µm) to expose a steel surface.

Electrochemical Measurements
The corrosion behaviour of deposited coatings was investigated in an aerated stagnant 0.5 M NaCl solution. All electrochemical measurements were performed at ambient temperature with an Autolab PGSTAT302 potentiostat (Metrohm AG, Herisau, Switzerland) using a standard three-electrode system with a Pt counter electrode and a saturated Ag/AgCl reference electrode. All potential values are reported versus this electrode. The corrosion current densities (i corr ) were determined from voltammetric measurements performed with the potential scan rate of 0.5 mV·s −1 from cathodic to anodic region.
The measurements of electrochemical impedance spectra (EIS) were performed at the open circuit potential with the FRA2 module applying a signal of 10 mV amplitude in the frequency range from 20 kHz to 0.001 Hz.

Morphology and Composition
A focused ion beam scanning electron microscope (FIB-SEM) system Helios Nanolab 650 (ThermoFisher Scientific, Hillsboro, OR, USA) with an energy dispersive X-ray (EDX) spectrometer INCA Energy 350 (Oxford Instruments, Abingdon, UK) and X-Max 20 (Oxford Instruments, Abingdon, UK) silicon drift detector was employed for imaging of the surface morphology, for cross-section preparation and imaging, as well as for investigations of chemical composition. The morphology of samples was examined using 2-3 keV energy secondary electrons, EDX spectra were obtained at 1.6 nA probe current and 20 kV high tension.
The same equipment was also used for the preparation of thin film samples for further examination in transmission electron microscope (TEM). TEM Tecnai G2 F20 X-TWIN (ThermoFisher Scientific, Hillsboro, OR, USA) with energy-dispersive X-ray spectrometer (EDX) with r-TEM detector was used for measurements of Ce, Mo, P, O and Fe concentration depth profiles in deposited coatings at 200 kV. A protective Pt layer of 1 µm thickness was deposited on a sample selected area of 20 µm × 3 µm before a cross-sectioning or sample preparation for TEM. A focussed Ga + ions beam was used in the sample cutting at 30 kV. Omniprobe Model 100.7 nanomanipulator (Oxford Instruments, Abingdon, UK) was applied for TEM lamella lift-off. Final thinning was performed on the attached to TEM grid lamella.
The X-ray photoelectron spectroscopy (XPS) studies were performed by a spectrometer ESCALAB (VG Scientific, East Grinstead, UK) using X-radiation of MgK α (1253.6 eV, pass energy of 20 eV). To obtain depth profiles, the samples were etched in the preparation chamber by ionized Ar at a vacuum of 5 × 10 −4 Pa. An accelerating voltage of ca. 1.0 kV and a beam current of 20 µA·cm −2 were used.

Formation of Conversion Coatings
In phosphating process, the surface of a carbon steel in contact with an acidic phosphate solution covers with a conversion layer, which contains a mixture of iron phosphate and oxide. According to potential-pH diagram of Fe in molybdate-containing solution, insoluble FeMoO 4 is formed at slightly acidic pH and the process takes place at the potentials, where active dissolution of Fe occurs [5]. The curve 1 in Figure 1 represents the evolution of the open-circuit potential (OCP) of steel electrode immersed in the phosphate solution containing Mo ions. The dissolution process of substrate is accompanied by a slight decrease in the potential values at the initial stage of the conversion coating formation, with the following stabilization at approximately −0.620 V (Ag/AgCl). This observation implies that ca. 20-30 min was enough to form phosphate/molybdate layer (Fe/P-Mo) on the steel surface.

Surface Morphology and Inner Structure
A cracked "dried riverbed" morphology is typical for the molybdate-containing conversion coatings, what has been reported by a number of authors [8,22,25] and such morphology is observed in the case of the deposited Fe/P-Mo coatings as well. SEM image of the sample is presented in Figure 2a. The presence of surface cracks in µm range or larger  As the protective and structural properties of Ce conversion coatings depend on the anionic composition of the deposition solution [12] two Ce(NO 3 ) 3 electrolytes, with and without sulphate ions, were applied. The potential evolution for Fe/Mo-P samples immersed in the 0.05 M Ce(NO 3 ) 3 and the 0.05 M Ce(NO 3 ) 3 + 0.025 M Na 2 SO 4 solutions are presented in Figure 1 (curves 2 and 3). In both solutions the formation of the conversion film led to an important ennoblement of the OCP values and after 20-30 min the potential plateaus around~−0.500 to −0.470 V (Ag/AgCl). This plateau suggests that the reaction occurring at the interface reached the steady state and that conversion process had been completed.

Surface Morphology and Inner Structure
A cracked "dried riverbed" morphology is typical for the molybdate-containing conversion coatings, what has been reported by a number of authors [8,22,25] and such morphology is observed in the case of the deposited Fe/P-Mo coatings as well. SEM image of the sample is presented in Figure 2a. The presence of surface cracks in µm range or larger could be related to the increase of stress induced by the film thickness. Alternatively, the cracks could form during the drying procedure performed at the end of the conversion process. The quality of deposited Fe/P-Mo coating appeared to be significantly influenced by the process duration. The increase in the conversion time up to 0.5 h led to the increase in the density of cracks in the film, therefore the process duration was limited to 20 min. According to the SEM image of the cross-section (Figure 2b), the Fe/P-Mo layer continuously covers steel surface, while its thickness varies in the range from 120 to 170 nm, with the average thickness value of ca. 150 nm. Meanwhile, the average thickness of a pure phosphate coating on steel surface, deposited in the same solution, was detected to be higher (200 nm) compared to Fe/P-Mo sample [26]. In addition, Mocontaining samples exhibited some cracks at the interface between conversion film and substrate ( Figure 2b).
As sulphates in Ce(NO 3 ) 3 solution act as grain refiners and growth inhibitors of the Ce-containing conversion layer [12], the latter conditions are expected to affect the surface morphology and inner structure of the Ce-modified Fe/P-Mo coating. SEM images of these coatings are presented in Figure 2c-f. Indeed, a non-uniform thickness of the conversion layer, which varied between 160 and 490 nm and the presence of randomly located additional crystalline aggregates, with dimensions between 0.5 and 2.5 µm, on the surface of it, were typical characteristics of the Fe/P-Mo-Ce1 coating, the top layer of which was deposited in a pure Ce(NO 3  in the density of cracks in the film, therefore the process duration was limited to 20 min. According to the SEM image of the cross-section (Figure 2b), the Fe/P-Mo layer continuously covers steel surface, while its thickness varies in the range from 120 to 170 nm, with the average thickness value of ca. 150 nm. Meanwhile, the average thickness of a pure phosphate coating on steel surface, deposited in the same solution, was detected to be higher (200 nm) compared to Fe/P-Mo sample [26]. In addition, Mo-containing samples exhibited some cracks at the interface between conversion film and substrate (Figure 2b). As sulphates in Ce(NO3)3 solution act as grain refiners and growth inhibitors of the Ce-containing conversion layer [12], the latter conditions are expected to affect the surface

Chemical Composition
The chemical composition of the investigated conversion coatings was analysed applying EDX and XPS techniques. Due to the moderate thickness of the conversion layer the EDX results obtained for the samples prepared for SEM analysis yielded reliable information only on the average concentrations of Mo, Ce, P, O and Fe in the deposited coatings (Table 1). While the amounts of P and Mo in all the investigated samples were very close and varied in the range between 1.2 at.% and 1.8 at.%, the concentration of Ce in the conversion layer was higher for coating deposited in sulphate-containing solution (2.28 at.%) compared to sample deposited in bare nitrate one (1.75 at.%). More precise information on the composition and, especially, on the distribution of the elements in the conversion layer can be obtained from EDX measurements of FIB-prepared thin film. TEM images of the cross-sections of investigated coatings with analyzed regions indicated and the element distribution profiles are presented in Figure 3a-f. The thickness of the conversion coatings due to both, initial steel surface morphology and peculiarities of the conversion process varies from place to place Figure 3a,c,d. However, it can be observed that Fe/P-Mo-Ce2 coatings deposited in sulphate-containing Ce solution were more compact with less number of the structural defects. (Figure 3e).
EDX analysis revealed that up to the depth of 120-150 nm of investigated conversion coatings the concentrations of Fe and Mo were very close and varied between 4 at.% and 7 at.%, while the amount of P varied in the range between 10 at.% and 18 at.% and was slightly higher for the Fe/P-Mo sample. The amount of Ce was detected to be higher in the sample deposited in the sulphate-containing solution as the maximal value reached up to 5 at.%, while for the sample deposited in bare Ce(NO 3 ) 3 solution this value was close to 3 at.%. Besides, Ce in Fe/P-Mo-Ce coatings was located in the outer part of the conversion layer and was detected up to the depth of 50 and 70 nm in Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2, respectively (Figure 3e,f).
The chemical state of the elements in the conversion coatings was characterized by XPS measurements. Taking into consideration the elements, which may be responsible for the self-healing capability of the conversion films, the oxidation states of Mo and Ce were analyzed. The high-resolution Mo 3d spectra of Fe/P-Mo and Fe/P-Mo-Ce samples were recorded after different times of the surface sputtering with Ar ions and are shown in Figure 4 for the depths of 20 and 60 nm. Even distribution of Mo in the Fe/P-Mo coating was observed up to the depth of 90 nm and concentration of this element was close to 11 at.%. As shown in Figure 4b, the Mo 3d spectrum can be deconvoluted into three peaks. The peaks at 232. 2 [22,25,27,28]. The molar ratio of Mo(VI) and Mo(IV) compounds was determined to be 3:2. EDX analysis revealed that up to the depth of 120-150 nm of investigated conversion coatings the concentrations of Fe and Mo were very close and varied between 4 at.% and 7 at.%, while the amount of P varied in the range between 10 at.% and 18 at.% and was slightly higher for the Fe/P-Mo sample. The amount of Ce was detected to be higher in the sample deposited in the sulphate-containing solution as the maximal value reached up to 5 at.%, while for the sample deposited in bare Ce(NO 3 ) 3 solution this value was close to 3 at.%. Besides, Ce in Fe/P-Mo-Ce coatings was located in the outer part of the conversion The chemical state of the elements in the conversion coatings was characterized by XPS measurements. Taking into consideration the elements, which may be responsible for the self-healing capability of the conversion films, the oxidation states of Mo and Ce were analyzed. The high-resolution Mo 3d spectra of Fe/P-Mo and Fe/P-Mo-Ce samples were recorded after different times of the surface sputtering with Ar ions and are shown in Figure 4 for the depths of 20 and 60 nm. Even distribution of Mo in the Fe/P-Mo coating was observed up to the depth of 90 nm and concentration of this element was close to 11 at.%. As shown in Figure 4b, the Mo 3d spectrum can be deconvoluted into three peaks. The peaks at 232. 2 [22,25,27,28]. The molar ratio of Mo(VI) and Mo(IV) compounds was determined to be 3:2. The chemical state of the elements in the conversion coatings was characterized by XPS measurements. Taking into consideration the elements, which may be responsible for   Meanwhile, the outer layers of Ce-modified Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings contained significantly lower amounts of Mo, the concentration of which varied from 2 to 4 at.%. The molar ratio of Mo(VI) and Mo(IV) compounds determined similarly as for Fe/P-Mo sample, in the case of Fe/P-Mo-Ce one was ~4:1 and was close to that stated by the authors of [22]. The latter results imply that during modification of Fe/P-Mo coating with Ce ions, the total amount of Mo in the outer layer of the coating decreases, while the fraction Mo(VI) increases.
The XPS spectra for the Ce 3d region recorded at the different depths of Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings are presented in Figure 5. The amount of Ce up to the depth of 40 nm varied between 7 at.%-10 at.% and 8 at.%-13 at.% for Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings, respectively. In the Ce 3d spectra, three different regions can be identified. The first one in the binding energy range from 880 to 890 eV corresponds to Ce 3d5/2, the second one at the binding energies from 890 to 910 eV includes the zone where the Ce 3d3/2 Meanwhile, the outer layers of Ce-modified Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings contained significantly lower amounts of Mo, the concentration of which varied from 2 to 4 at.%. The molar ratio of Mo(VI) and Mo(IV) compounds determined similarly as for Fe/P-Mo sample, in the case of Fe/P-Mo-Ce one was~4:1 and was close to that stated by the authors of [22]. The latter results imply that during modification of Fe/P-Mo coating with Ce ions, the total amount of Mo in the outer layer of the coating decreases, while the fraction Mo(VI) increases.
The XPS spectra for the Ce 3d region recorded at the different depths of Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings are presented in Figure 5. The amount of Ce up to the depth of 40 nm varied between 7 at.%-10 at.% and 8 at.%-13 at.% for Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings, respectively. In the Ce 3d spectra, three different regions can be identified. The first one in the binding energy range from 880 to 890 eV corresponds to Ce 3d 5/2 , the second one at the binding energies from 890 to 910 eV includes the zone where the Ce 3d 3/2 and Ce 3d 5/2 spectra overlap, and the third one is due to the emergence of the satellite peak Coatings 2021, 11,194 9 of 15 associated with Ce 3d 3/2 at a binding energy value close to 917.0 eV [10][11][12]. This peak is of a crucial importance for determination of the oxidation state of cerium because its presence is only associated with Ce (IV). The percentage of Ce(IV) was calculated according to the equation [29]: where µ is the percentage of the satellite peak area at 916.7 eV with respect to the total Ce 3d peak area. and Ce 3d5/2 spectra overlap, and the third one is due to the emergence of the satellite peak associated with Ce 3d3/2 at a binding energy value close to 917.0 eV [10][11][12]. This peak is of a crucial importance for determination of the oxidation state of cerium because its presence is only associated with Ce (IV). The percentage of Ce(IV) was calculated according to the equation [29]: where µ is the percentage of the satellite peak area at 916.7 eV with respect to the total Ce 3d peak area. It should be noted that there might be some errors in the data regarding determined Ce(III)/Ce(IV) ratio, due to the possibility of the reduction of Ce(IV) to Ce(III) during Ar sputtering. However, it is obvious, that up to the depth of 40 nm, sample Fe/P-Mo-Ce2 exhibited ~20% ± 5% higher percentage of Ce(IV) with respect to the total Ce quantity compared to sample Fe/P-Mo-Ce1.
Cerium conversion coatings can thus be described as a mixture of Ce(III) and Ce(IV) compounds, while the presence of SO4 2− ions in the Ce deposition solution leads to higher amount of Ce compounds in the coating as well as higher percentage of Ce in the higher oxidation state. XPS data indicated as well, that the addition of SO4 2− to the conversion solution leads to an incorporation of up to 1 at.% of S into the coating.

Protective Ability
The protective ability of investigated conversion coatings was evaluated on the basis of voltammetric measurements, which were carried out in 0.5 M NaCl solution. The polarization curves of the investigated samples are shown in Figure 6, while the values of the corrosion current (icorr) densities, determined from Tafel line extrapolation and other electrochemical parameters are listed in Table 2. Fe/P-Mo-Ce2 samples exhibited the lowest values of icorr among all the investigated coatings (~2.7 × 10 −7 A·cm −2 ), whereas corrosion current densities of Fe/P-Mo and Fe/P-Mo-Ce1 samples were close enough and were higher by an order of magnitude (~2 × 10 −6 A·cm −2 ). The protective efficiency of the coatings, P%, was calculated according to the equation [11,12]: (2) It should be noted that there might be some errors in the data regarding determined Ce(III)/Ce(IV) ratio, due to the possibility of the reduction of Ce(IV) to Ce(III) during Ar sputtering. However, it is obvious, that up to the depth of 40 nm, sample Fe/P-Mo-Ce2 exhibited~20% ± 5% higher percentage of Ce(IV) with respect to the total Ce quantity compared to sample Fe/P-Mo-Ce1.
Cerium conversion coatings can thus be described as a mixture of Ce(III) and Ce(IV) compounds, while the presence of SO 4 2− ions in the Ce deposition solution leads to higher amount of Ce compounds in the coating as well as higher percentage of Ce in the higher oxidation state. XPS data indicated as well, that the addition of SO 4 2− to the conversion solution leads to an incorporation of up to 1 at.% of S into the coating.

Protective Ability
The protective ability of investigated conversion coatings was evaluated on the basis of voltammetric measurements, which were carried out in 0.5 M NaCl solution. The polarization curves of the investigated samples are shown in Figure 6, while the values of the corrosion current (i corr ) densities, determined from Tafel line extrapolation and other electrochemical parameters are listed in Table 2. Fe/P-Mo-Ce2 samples exhibited the lowest values of i corr among all the investigated coatings (~2.7 × 10 −7 A·cm −2 ), whereas corrosion current densities of Fe/P-Mo and Fe/P-Mo-Ce1 samples were close enough and were higher by an order of magnitude (~2 × 10 −6 A·cm −2 ). The protective efficiency of the coatings, P%, was calculated according to the equation [11,12]: Coatings 2021, 11,194 10 of 15 where i o corr and i corr denote the corrosion current density of the bare steel and that of the electrode with the conversion coating, respectively. The calculated value of P% increased from 59% for Fe/P-Mo sample up to 95% for Fe/P-Mo-Ce2. It is obvious that Ce conversion coating deposited in a sulphate-containing media exhibited the highest protective ability among the coatings investigated. The comparable protective abilities of Fe/P-Mo and Fe/P-Mo-Ce1 and similarity of the composition between Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings, implies that higher protective ability of the conversion layer is related probably with the structural parameters rather than with the composition of the coating. The latter observation can be corroborated by the results of our previous studies, where similar higher values of i corr (1.6-1.7 × 10 −6 A·cm −2 ) were determined for Ce layers deposited directly on a bare or phosphated steel surface [26]. In addition, the latter samples possessed similar structural defects like Fe/P-Mo and Fe/P-Mo-Ce1 coating. It seems that fine crystals of Fe/P-Mo-Ce2 conversion film facilitate the coverage of the coating, what yields homogeneous distribution of the conversion layer on steel surface resulting in a lower number of structural defects, what, in turn, improves the corrosion resistance of the conversion coating. As the average thickness of Fe/P-Mo-Ce2 was the lowest among the conversion coatings investigated, it can be assumed that coating thickness is not always a reliable indicator of corrosion resistance, because the thickest Fe/P-Mo-Ce1 did not perform well in corrosion tests.
where i o corr and icorr denote the corrosion current density of the bare steel and that of the electrode with the conversion coating, respectively. The calculated value of P% increased from 59% for Fe/P-Mo sample up to 95% for Fe/P-Mo-Ce2. It is obvious that Ce conversion coating deposited in a sulphate-containing media exhibited the highest protective ability among the coatings investigated. The comparable protective abilities of Fe/P-Mo and Fe/P-Mo-Ce1 and similarity of the composition between Fe/P-Mo-Ce1 and Fe/P-Mo-Ce2 coatings, implies that higher protective ability of the conversion layer is related probably with the structural parameters rather than with the composition of the coating. The latter observation can be corroborated by the results of our previous studies, where similar higher values of icorr (1.6-1.7 × 10 −6 A·cm −2 ) were determined for Ce layers deposited directly on a bare or phosphated steel surface [26]. In addition, the latter samples possessed similar structural defects like Fe/P-Mo and Fe/P-Mo-Ce1 coating. It seems that fine crystals of Fe/P-Mo-Ce2 conversion film facilitate the coverage of the coating, what yields homogeneous distribution of the conversion layer on steel surface resulting in a lower number of structural defects, what, in turn, improves the corrosion resistance of the conversion coating. As the average thickness of Fe/P-Mo-Ce2 was the lowest among the conversion coatings investigated, it can be assumed that coating thickness is not always a reliable indicator of corrosion resistance, because the thickest Fe/P-Mo-Ce1 did not perform well in corrosion tests.

Self-Healing Ability
In order to assess the self-healing ability of investigated conversion coatings, a set of studies were carried out on samples with partially removed conversion layer, what was done by mechanical scratching with a sharp metallic needle. The average chemical composition of the areas in the fresh scratches (areas 1 and 2 in Figure 7a) was determined by EDX measurements and it was found to be close to the steel composition, while the results obtained in the analysed areas 3 and 4 ( Figure 7a) were close to those, presented in Table 1. These samples were immersed into aerated 0.5 M NaCl solution for up to 4 h and SEM analysis of the surface morphology was carried out afterwards. The obvious differences in the sample corrosion behaviour were observed. Even after one hour of exposure Fe/P-Mo coating exhibited the abundant presence of steel corrosion products formed in the scratched area (Figure 7b). After 4 h exposure Fe/P-Mo-Ce1 sample showed the signs of initial corrosion damages (Figure 7c), whereas no corrosion traces were found on the sample Fe/P-Mo-Ce 2 (Figure 7d). The obtained results allow to presume that both conversion coatings with Ce compounds possess self-healing ability under the experimental conditions applied and this ability was expressed largely for the coating deposited in a sulphate containing solution.

Self-Healing Ability
In order to assess the self-healing ability of investigated conversion coatings, a set of studies were carried out on samples with partially removed conversion layer, what was done by mechanical scratching with a sharp metallic needle. The average chemical composition of the areas in the fresh scratches (areas 1 and 2 in Figure 7a) was determined by EDX measurements and it was found to be close to the steel composition, while the results obtained in the analysed areas 3 and 4 ( Figure 7a) were close to those, presented in Table 1. These samples were immersed into aerated 0.5 M NaCl solution for up to 4 h and SEM analysis of the surface morphology was carried out afterwards. The obvious differences in the sample corrosion behaviour were observed. Even after one hour of exposure Fe/P-Mo coating exhibited the abundant presence of steel corrosion products formed in the scratched area (Figure 7b). After 4 h exposure Fe/P-Mo-Ce1 sample showed the signs of initial corrosion damages (Figure 7c), whereas no corrosion traces were found on the sample Fe/P-Mo-Ce 2 (Figure 7d). The obtained results allow to presume that both conversion coatings with Ce compounds possess self-healing ability under the experimental conditions applied and this ability was expressed largely for the coating deposited in a sulphate containing solution. The EIS technique is a useful tool, which can provide important information on the physical-chemical processes occurring on the coated sample during immersion in the corrosive media. An evolution of the impedance spectra for Fe/P-Mo and Fe/P-Mo-Ce2 sam- The EIS technique is a useful tool, which can provide important information on the physical-chemical processes occurring on the coated sample during immersion in the corrosive media. An evolution of the impedance spectra for Fe/P-Mo and Fe/P-Mo-Ce2 samples with defects after different periods of immersion in the 0.5 M NaCl solution are presented in Figures 8 and 9. When Fe/P-Mo sample was scratched the impedance values tend to decrease at all frequencies when the immersion time increased without any signs of recovery (Figure 8). The decrease in impedance is caused by permanent development of corrosion processes in defect zone. The latter results imply that Fe/P-Mo coatings were not capable of self-repair.
Coatings 2021, 11, x FOR PEER REVIEW 12 of ples with defects after different periods of immersion in the 0.5 M NaCl solution are pr sented in Figures 8 and 9. When Fe/P-Mo sample was scratched the impedance value tend to decrease at all frequencies when the immersion time increased without any sign of recovery ( Figure 8). The decrease in impedance is caused by permanent developmen of corrosion processes in defect zone. The latter results imply that Fe/P-Mo coatings wer not capable of self-repair.  The EIS spectra of Fe/P-Mo-Ce2 sample with artificial defect are presented in Figure  A drop of impedance at low frequencies occurs during the initial period of immersio This drop is related to the breakdown of the coating and the onset of corrosion activity o the exposed metal surface. However, after ~1 h impedance, values start increasing agai towards the initial ones. The increase of the low-frequency impedance implies the activ  Figures 8 and 9. When Fe/P-Mo sample was scratched the impedance valu tend to decrease at all frequencies when the immersion time increased without any sig of recovery ( Figure 8). The decrease in impedance is caused by permanent developme of corrosion processes in defect zone. The latter results imply that Fe/P-Mo coatings we not capable of self-repair.  The EIS spectra of Fe/P-Mo-Ce2 sample with artificial defect are presented in Figure  A drop of impedance at low frequencies occurs during the initial period of immersio This drop is related to the breakdown of the coating and the onset of corrosion activity o the exposed metal surface. However, after ~1 h impedance, values start increasing aga towards the initial ones. The increase of the low-frequency impedance implies the acti The EIS spectra of Fe/P-Mo-Ce2 sample with artificial defect are presented in Figure 9. A drop of impedance at low frequencies occurs during the initial period of immersion. This drop is related to the breakdown of the coating and the onset of corrosion activity on the exposed metal surface. However, after~1 h impedance, values start increasing again towards the initial ones. The increase of the low-frequency impedance implies the active corrosion protection. Thus, these results suggest that the presence of Ce in the molybdate coating can lead to increase of low-frequency impedance due to the healing of defect.