Effect of 6-Aminohexanoic Acid Released from Its Aluminum Tri-Polyphosphate Intercalate (ATP-6-AHA) on the Corrosion Protection Mechanism of Steel in 3.5% Sodium Chloride Solution

A new corrosion inhibitor called ATP-6-AHA was elaborated, and its inhibition action on S235 low carbon steel in 3.5% sodium chloride (NaCl) was investigated using gravimetry, potentiodynamic polarization (PP), and electrochemical impedance spectroscopy (EIS). The release of ecofriendly 6-aminohexanoic acid (6-AHA) from its established aluminum tri-polyphosphate intercalate (ATP-6-AHA) is investigated using electrochemical and surface characterization techniques such as X-ray diffraction (XRD) and X-ray fluorescence (XRF). The results revealed that ATP-6-AHA is a good inhibitor, with an inhibition efficiency of approximately 70%. The efficiency is related to the passivation of a steel surface by a phosphate protective layer due to the synergistic effect of 6-AHA, as confirmed by a steel surface analysis conducted using X-ray photoelectron spectroscopy (XPS) and scanning electron microscopy (SEM). This study suggests that the intercalation of 6-AHA as a sustainable organic molecule within the interlayer spaces of aluminum tri-polyphosphate can well serve as a good flaky inhibitor for protecting S235 low-carbon steel from corrosion in 3.5% NaCl.


Introduction
Carbon steel is widely used in several industrial applications due to its outstanding mechanical properties and low cost [1]. However, this material is subject to corrosion in aggressive environments, such as marine media [2,3]. One method to decrease the rate of iron dissolution that is frequently applied is the use of corrosion inhibitors [4][5][6]. Among the non-toxic compounds that are, aluminum dihydrogen tri-polyphosphate (ATP) has been shown to be a good candidate for steel [7]. However, ATP has high acidity and low solubility, affecting the long-term storage stability of the coated systems [8]. Therefore, a large number of studies have been performed to modify this layered phosphate compound by introducing different additives [7]. Among others, 6-aminohexanoic acid (6-AHA) is an organic, aqueous soluble molecule comprising polar nitrogen and oxygen atoms as well as double bonds in its molecular structure and has been tested as a corrosion inhibitor for mild steel in hydrochloride solution, showing enhanced corrosion protection, as reported by M. Abdeli et al. [9]. In addition, the organic molecule of 6-aminohexanoic acid (6-AHA) has been intercalated into the interlayer space of layered ATP, as recently shown by some of the authors [10]. In this work, ATP and ATP-6-AHA were characterized by different characterization techniques (XRD, TGA (thermogravimetric analysis), SEM, Infrared and Raman spectroscopy). The interlayer space of ATP was expanded by 10.1 Å, with the 6-AHA planes arranged in bilayers [10]. No investigation has been conducted regarding the deintercalation of 6-AHA from the ATP-6-AHA hybrid material nor on the contribution of the 6-amino hexanoic acid (6-AHA) to the protection mechanism of S235 low-carbon steel.
For many years, ATP was mainly used as an anticorrosive additive in coatings and was preferential to the less environmentally friendly lead and chromium alternatives. Several works have been published in this sense. An inorganic coating that was created by combining chemically bonded phosphate ceramic (CBPC) binder and aluminum tripolyphosphate (ATP) pigment was designed and prepared for the anti-corrosion treatment of steel, showing enhanced corrosion protection [11]. X. Lu et al. showed that the protective performance of a Mg-rich primer on an AZ91D magnesium alloy was greatly improved with the addition of aluminum di-hydrogen tripolyphosphate pigment into the primer [12].
Song et al. evaluated the influence of aluminum di-hydrogen tripolyphosphate on the protective behavior of an acrylic water-based paint applied to rusty steels. The electrochemical results obtained using an EIS of scratched steel for 500 h of immersion in 3.5% NaCl solution showed evidence of good anticorrosive performance, with no rust, blisters, flakes, or cracks occurring on the coating compared to the epoxy antirust coatings. The LEIS (local electrochemical impedance spectroscopy) measurements performed in 3.5% NaCl showed that the coatings exhibited electrochemical activity at the beginning of immersion; as such, the mechanism of protection is due to an iron phosphate layer, leading to an increase in the coating resistance [13].
For ATP-6-AHA, further studies are needed to explain the inhibition mechanism that is induced by the release of 6-AHA into the corrosive medium in order to promote the formation of an iron phosphate film. As a consequence, the purpose of the current work is to confirm the deintercalation of 6-AHA after electrochemical impedance spectroscopy (EIS) testing using X-ray diffraction (XRD) and X-ray fluorescence (XRF).
We have already tested the application of this material in our previous work using 0.1 M (NaCl) medium, but we did not conduct an extensive investigation for higher concentrations [10]. A 3.5% NaCl solution has been used as an electrolyte in several corrosion inhibitor studies [14,15], which to some extent, simulate an actual corrosive solution. In view of the above observations and as a continuation of our work on understanding the protection mechanism of ATP-6-AHA, we report a more in-depth study to examine the corrosion-inhibiting ability of this new phosphate compound in an aggressive environment, such as in a 3.5% NaCl aerated solution. The inhibition efficiency of the aluminum tri-polyphosphate intercalated 6-aminohexanoic acid (ATP-6-AHA) was investigated by means of the gravimetric method and through electrochemical measurements using open circuit potential (OCP), potentiodynamic polarization (PP), and EIS and showed an enhanced corrosion resistance for S235 low-carbon steel in the presence of ATP-6-AHA, with an inhibition efficiency of approximately 70%. The protection mechanism was evaluated using X-ray photoelectron spectroscopy (XPS) and a scanning electron microscope (SEM). It was in this way that a protective layer was deposited onto steel surface, which occurred as a result of the synergistic effect of the released 6-AHA from ATP-6-AHA with aluminum phosphate anions.

ATP-6-AHA Synthesis Procedure
The necessary precursor, aluminum dihydrogen tri-polyphosphate (AlH 2 P 3 O 10 ·2H 2 O), was synthesized according to our previous protocol and according to Rishi et al. [10,13]. Alumina oxide and phosphoric acid (mole ratio P 2 O 5 /Al 2 O 3 is 3:1) were mixed until the mixture became viscous. The slurry was then transferred into a reacting furnace and was heated up to 240 • C for 24 h. The obtained solid was taken out of the furnace and was washed many times using deionized water until the filtrate became clear and had an acidic pH∼3; it was subsequently dried and was finally ground using an agate mortar into fine powders. The intercalation of 6-aminohexanoic acid (NH 2 (CH 2 ) 5 CO 2 H, 99%, Sigma Aldrich, Taufkirchen, Germany), was carried out by mixing 0.5 g of ATP with 6-aminohexanoic acid (0.5 M). The slurry was stirred at room temperature (RT) for 24 h. The obtained compound was filtered, washed with double distilled water, centrifuged, and dried under ambient conditions for 24 h [10].
XPS steel surface analysis was performed by a KRATOS AXIS Ultra DLD (Kratos Analytical, Manchester, UK) assembled with a monochromatic Al Kα anode performing at 15 kV (225 W). For the survey spectra, a pass energy of 160 eV was used, while for the region spectra, it was 40 eV. The investigated area was 700 µm × 300 µm. For all of the steel samples, charge neutralization was necessary. The evaluation and validation of the data were achieved using the CASA-XPS software (software version 2.3.18, Casa Software Ltd., Manchester, UK). The spectra were calibrated by adjusting the C1s signal to 284.5 eV. For the deconvolution of the region files, background subtraction (linear or Shirley) was performed before calculation.
The surface morphology of the S235 steel surface in sodium chloride with the ATP-6-AHA inhibitor was examined using a scanning electron microscope (TESCAN Vega TC X64, Brno, Czech Republic) equipped with an energy dispersive X-ray (EDX) spectrometer for the elemental composition analysis of the samples from eumeX (XRFSystems, Heidenrod, Germany).

Materials and Low Carbon Steel Surface Preparation
The chemical composition by weight % of the low-carbon steel (S235 (E24), El Jadida, Morocco) used in this study was as follows: S: 0.020, P: 0.017, Mn: 0.457, Cu: 0.301, Si: 0.114, Mo: 0.023, Ni: 0.076, C: 0.111, and Fe as balance [10]. Before each electrochemical experiment, the exposed steel area was polished with different grades of emery papers (120, 800, and 2400 grit), rinsed with distilled water, and degreased with acetone before being transferred to the measurement cell. The corrosive 3.5% NaCl solution was prepared using analytical reagent-grade chemicals (sodium chloride, 99%, SOLVACHIM, Germany) and distilled water in order to obtain a blank solution and a 0.18 g/L concentration of the ATP-6-AHA phosphate-based compound for the ATP-6-AHA solution.

Corrosion Tests
The gravimetric method is an effective non-electrochemical technique that requires the exposure of the steel samples in the solution under study for a specific time period. The corrosion rate (CR) expressed in mm/y (Equation (1)) of the current S235 steel samples was evaluated after 20 h of immersion in 3.5% NaCl with and without ATP-6-AHA [16].
where (W) is the weight loss of the S235 steel specimen, (a) is the exposed surface area of the specimen, (t) is the immersion time (20 h), and (D) is the S235 steel density. Electrochemical tests were performed in a three-electrode glass cell at room temperature (25 • C). A platinum counter electrode and a saturated calomel reference electrode (SCE) were used in all of the electrochemical experiments performed using a SP150 Bi-oLogic potentiostat/galvanostat. The corrosion potential was recorded during 20 h of immersion time, and the polarization plots were made with and without ATP-6-AHA at a scanning speed of 1 mV s −1 . Impedance plots were acquired using 10 mV (RMS) sinusoidal perturbation in the frequency range from 10 5 to 10 −2 Hz, with nine points per frequency decade. The EIS measurements were executed after 20 h of immersion time.

Chemical Composition
The XRD spectra of ATP, ATP-6-AHA, and the deintercalated form 6-AHA-ATP are shown in Figure 1. The layered structure of the ATP was confirmed by the presence of the intense (001) peak of the AlH 2 P 3 O 10 ·2H 2 O (ref code: 96-710-0708) phase at 2θ = 11.2, corresponding to a basal spacing of 0.79 nm, and consistent with previous data reported by Rishi et al. [17]. The increase in the basal distance of approximately 1 nm in the ATP-6-AHA diffractogram can be attributed to an expansion of the interlayer spacing for the host ATP through the intercalation of the organic 6-AHA. A new phase appears after intercalation, with a d 001 basal spacing of 1.79 nm. According to the XRD pattern of ATP-6-AHA after the EIS test, after the deintercalation [10], the upper spectrum in Figure 1 shows a large decrease in the (001) characteristic peak of ATP-6-AHA, with the appearance of a new phase of Na 2 AlP 3 O 10 ·4H 2 O (ref code: 00-036-0262), which clearly confirms the release of 6-AHA from ATP-6-AHA during the EIS test in sodium chloride.
where (W) is the weight loss of the S235 steel specimen, (a) is the exposed surface area of the specimen, (t) is the immersion time (20 h), and (D) is the S235 steel density. Electrochemical tests were performed in a three-electrode glass cell at room temperature (25 °C). A platinum counter electrode and a saturated calomel reference electrode (SCE) were used in all of the electrochemical experiments performed using a SP150 Bio-Logic potentiostat/galvanostat. The corrosion potential was recorded during 20 h of immersion time, and the polarization plots were made with and without ATP-6-AHA at a scanning speed of 1 mV s −1 . Impedance plots were acquired using 10 mV (RMS) sinusoidal perturbation in the frequency range from 10 5 to10 −2 Hz, with nine points per frequency decade. The EIS measurements were executed after 20 h of immersion time.

Chemical Composition
The XRD spectra of ATP, ATP-6-AHA, and the deintercalated form 6-AHA-ATP are shown in Figure 1. The layered structure of the ATP was confirmed by the presence of the intense (001) peak of the AlH2P3O10•2H2O (ref code: 96-710-0708) phase at 2θ = 11.2, corresponding to a basal spacing of 0.79 nm, and consistent with previous data reported by Rishi et al. [17]. The increase in the basal distance of approximately 1 nm in the ATP-6-AHA diffractogram can be attributed to an expansion of the interlayer spacing for the host ATP through the intercalation of the organic 6-AHA. A new phase appears after intercalation, with a d001 basal spacing of 1.79 nm. According to the XRD pattern of ATP-6-AHA after the EIS test, after the deintercalation [10], the upper spectrum in Figure 1 shows a large decrease in the (001) characteristic peak of ATP-6-AHA, with the appearance of a new phase of Na2AlP3O10⋅4H2O (ref code: 00-036-0262), which clearly confirms the release of 6-AHA from ATP-6-AHA during the EIS test in sodium chloride.  The chemical composition of ATP, ATP-6-AHA, and the deintercalated form was determined by XRF spectroscopy. The chemical composition in Table 1 shows that phosphates and alumina (Al 2 O 3 ) are the major chemical constituents of ATP. This composition decreases after the intercalation of 6-AHA; moreover, a larger decrease was noticed for the deintercalated form.

Gravimetric and Electrochemical Measurements
The corrosion tests showed that the CR in the blank sodium chloride solution is 0.21 mm/year. This rate decreases to 0.072 mm/year after the addition of ATP-6-AHA with a concentration of 0.18 g/L. The inhibiting effect of ATP-6-AHA on the corrosion of S235 low-carbon steel was determined by evaluating the inhibition efficiency η(%) according to Equation (2): where CR(blank) and CR(ATP-6-AHA) denote the corrosion rate calculated using the gravimetric method in the 3.5% NaCl solution with and without ATP-6-AHA. Figure 2a shows the evolution of the S235 low-carbon steel potential as a function of immersion time in the 3.5% NaCl solution with and without ATP-6-AHA. The curves reveal that the presence of ATP-6-AHA in the corrosive medium increases the corrosion potential, which is approximately 70 mV higher than that in blank solution.
Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW The chemical composition of ATP, ATP-6-AHA, and the deintercalated form w termined by XRF spectroscopy. The chemical composition in Table 1 shows that phates and alumina (Al2O3) are the major chemical constituents of ATP. This comp decreases after the intercalation of 6-AHA; moreover, a larger decrease was notic the deintercalated form.

Gravimetric and Electrochemical Measurements
The corrosion tests showed that the CR in the blank sodium chloride solution mm/year. This rate decreases to 0.072 mm/year after the addition of ATP-6-AHA concentration of 0.18 g/L. The inhibiting effect of ATP-6-AHA on the corrosion o low-carbon steel was determined by evaluating the inhibition efficiency η(%) acc to Equation (2): where CR(blank) and CR(ATP-6-AHA) denote the corrosion rate calculated usi gravimetric method in the 3.5% NaCl solution with and without ATP-6-AHA. Figure 2a shows the evolution of the S235 low-carbon steel potential as a func immersion time in the 3.5% NaCl solution with and without ATP-6-AHA. The cur veal that the presence of ATP-6-AHA in the corrosive medium increases the cor potential, which is approximately 70 mV higher than that in blank solution. After the S235 steel/electrolyte interface had been stabilized for 20 h in the pr of ATP-6-AHA, the polarization curves in Figure 2b show that the corrosion poten the steal increased by nearly 70 mV compared to the blank one. The current dens creased from 18.5 µA⋅cm -2 for the blank one compared to 6.2 µA⋅cm -2 for the ATP-6 solution ( Table 2), which corresponds to an inhibition efficiency of 66%. The cathod rent increased slightly as a result of the inhibitor addition. This could be related decrease of the pH of the electrolyte accelerating the hydrogen evolution kinetics. results indicate that ATP-6-AHA phosphate mainly prevents the anodic reaction corrosion process. After the S235 steel/electrolyte interface had been stabilized for 20 h in the presence of ATP-6-AHA, the polarization curves in Figure 2b show that the corrosion potential of the steal increased by nearly 70 mV compared to the blank one. The current density decreased from 18.5 µA·cm −2 for the blank one compared to 6.2 µA·cm −2 for the ATP-6-AHA solution (Table 2), which corresponds to an inhibition efficiency of 66%. The cathodic current increased slightly as a result of the inhibitor addition. This could be related to the decrease of the pH of the electrolyte accelerating the hydrogen evolution kinetics. These results indicate that ATP-6-AHA phosphate mainly prevents the anodic reaction of the corrosion process. The Bode spectra in Figure 3 do not show differences at high frequencies beyond 10 3 Hz, indicating similar impedance behavior due to the resistance of the solution. The spectra are characterized by two well-defined relaxation processes. The time constant at about 1-10 Hz is related to the charge transfer process and the double-layer capacitance, while the low-frequency relaxation most probably originates from the diffusion limitations. Nevertheless, the impedance modulus measured at low frequencies (10 −2 Hz) and that is associated with the polarization resistances Rp discloses that the presence of ATP-6-AHA makes it possible to multiply the polarization resistance of the steel surface by a factor of 2.
The gravimetric and electrochemical measurements revealed an enhanced corrosion inhibition performance of ATP-6-AHA, which can be attributed to the formation of a porous film composed of iron phosphate, as shown by the XPS and SEM steel surface analysis below.  The Bode spectra in Figure 3 do not show differences at high frequencies beyond 10 3 Hz, indicating similar impedance behavior due to the resistance of the solution. The spectra are characterized by two well-defined relaxation processes. The time constant at about 1-10 Hz is related to the charge transfer process and the double-layer capacitance, while the low-frequency relaxation most probably originates from the diffusion limitations. Nevertheless, the impedance modulus measured at low frequencies (10 −2 Hz) and that is associated with the polarization resistances Rp discloses that the presence of ATP-6-AHA makes it possible to multiply the polarization resistance of the steel surface by a factor of 2.
The gravimetric and electrochemical measurements revealed an enhanced corrosion inhibition performance of ATP-6-AHA, which can be attributed to the formation of a porous film composed of iron phosphate, as shown by the XPS and SEM steel surface analysis below.

XPS Analysis of Corrosion Products
A detailed XPS investigation on each exposed S235 low-carbon steel surface was conducted. Figure 4 presents the whole survey, from 0 to 1300 eV of steel without inhibitor to the S235 steel surface after immersion tests in the 3.5% NaCl solution using ATP-6-AHA taking place over the course of five days. From the XPS spectrum in (Figure 4a), the main elements in the rust matrix for the steel surface without inhibitor are Fe, O, C, and Na. The peaks of Fe 2p appear in the region between 709 to ~734 eV. As shown in Figure 5, the electron binding energy centers of Fe 2p3/2 and Fe 2p1/2 at 711.3 and 728 eV, respectively, fulfill the standard data of Fe2O3 [15]. The binding energy of 719 eV is a shakeup with an

XPS Analysis of Corrosion Products
A detailed XPS investigation on each exposed S235 low-carbon steel surface was conducted. Figure 4 presents the whole survey, from 0 to 1300 eV of steel without inhibitor to the S235 steel surface after immersion tests in the 3.5% NaCl solution using ATP-6-AHA taking place over the course of five days. From the XPS spectrum in (Figure 4a), the main elements in the rust matrix for the steel surface without inhibitor are Fe, O, C, and Na. The peaks of Fe 2p appear in the region between 709 to~734 eV. As shown in Figure 5, the electron binding energy centers of Fe 2p 3/2 and Fe 2p 1/2 at 711.3 and 728 eV, respectively, fulfill the standard data of Fe 2 O 3 [15]. The binding energy of 719 eV is a shakeup with an associated Fe 2p 3/2 satellite peak, which is a fingerprint of the electronic structure of Fe 3+ [18,19]. Furthermore, another satellite peak can be observed at 734 eV, which can be assigned to Fe 2p 1/2 [20].
Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 7 associated Fe 2p3/2 satellite peak, which is a fingerprint of the electronic structure of Fe 3+ [18,19]. Furthermore, another satellite peak can be observed at 734 eV, which can be assigned to Fe 2p1/2 [20].  The presence of iron oxides and hydroxides can be confirmed from the O 1s spectra ( Figure 5). The oxygen signal is composed of three peaks. The first peak at 530.5 eV (green, Figure 5) is assigned to iron oxides [20], while the second at 531.5 eV(brown, Figure 5) is due to the presence of the (OH -) ions attributed to the iron oxy-hydroxides FeO(OH) [21], as verified by the XRD of the corroded S235 steel surface. The third peak at 533.5 eV (blue, Figure 5) has a lower intensity in comparison, which can be assigned to the adsorbed water molecules [21]. The carbon line (C 1s) has four main peaks, as described in Figure 5. The dominant peak was assessed at a binding energy of 285 eV(brown, Figure 5). The peak observed at 286 eV(purple, Figure 5), known as single bonded carbon C-C, is generally related to the contaminants that are common in XPS analysis due to the hydrocarbons that are present in the environment [22]. However, the two peaks observed at higher energy associated Fe 2p3/2 satellite peak, which is a fingerprint of the electronic structure of Fe 3+ [18,19]. Furthermore, another satellite peak can be observed at 734 eV, which can be assigned to Fe 2p1/2 [20].  The presence of iron oxides and hydroxides can be confirmed from the O 1s spectra ( Figure 5). The oxygen signal is composed of three peaks. The first peak at 530.5 eV (green, Figure 5) is assigned to iron oxides [20], while the second at 531.5 eV(brown, Figure 5) is due to the presence of the (OH -) ions attributed to the iron oxy-hydroxides FeO(OH) [21], as verified by the XRD of the corroded S235 steel surface. The third peak at 533.5 eV (blue, Figure 5) has a lower intensity in comparison, which can be assigned to the adsorbed water molecules [21]. The carbon line (C 1s) has four main peaks, as described in Figure 5. The dominant peak was assessed at a binding energy of 285 eV(brown, Figure 5). The peak observed at 286 eV(purple, Figure 5), known as single bonded carbon C-C, is generally related to the contaminants that are common in XPS analysis due to the hydrocarbons that are present in the environment [22]. However, the two peaks observed at higher energy The presence of iron oxides and hydroxides can be confirmed from the O 1s spectra ( Figure 5). The oxygen signal is composed of three peaks. The first peak at 530.5 eV (green, Figure 5) is assigned to iron oxides [20], while the second at 531.5 eV(brown, Figure 5) is due to the presence of the (OH − ) ions attributed to the iron oxy-hydroxides FeO(OH) [21], as verified by the XRD of the corroded S235 steel surface. The third peak at 533.5 eV (blue, Figure 5) has a lower intensity in comparison, which can be assigned to the adsorbed water molecules [21]. The carbon line (C 1s) has four main peaks, as described in Figure 5. The dominant peak was assessed at a binding energy of 285 eV(brown, Figure 5). The peak observed at 286 eV(purple, Figure 5), known as single bonded carbon C-C, is generally related to the contaminants that are common in XPS analysis due to the hydrocarbons that are present in the environment [22]. However, the two peaks observed at higher energy (~289 eV) (green and blue, Figure 5) correspond to carbon double-bonded oxygen C=O [23]. Moreover, the Na 1s spectrum could be fitted to one component at 1071.1 eV that is related to the presence of Na + -ions [24].
The chemical composition and oxidation states of a low-carbon steel surface with ATP-6-AHA are shown in Figure 6, which demonstrates core level peaks for Fe 2p, O 1s, P 2p, C 1s, and N 1s. The Fe 2p spectrum in Figure 6 shows the respective binding energies of 712 and 719 eV for Fe 2p 3/2 and Fe 2p 1/2 along with their respective satellite contributions at 719 and 734 eV, which can be assigned to Fe 2 O 3 [21] and FePO 4 [20], respectively. The high-resolution spectrum of O 1s exhibits three peaks at 530 (green, Figure 6), 532.5 (brown, Figure 6), and 534 eV (blue, Figure 6). These results clearly demonstrate the presence of Fe 2 O 3 and FePO 4 , which is in good agreement with Fe 2p 3/2 [20]. The O-peak from 6-AHA is likely included in the OH peak at 532.5 eV, as the O 1s peak of organic molecules has been reported to appear at this energy level [25]. The C 1s spectrum contain three components overall: (a) 285.5 eV (brown, Figure 6) corresponding to the covalent C-C bond of the adsorbed organic molecule [25] and carbon adsorbed from contaminants [22]; (b) 286 eV (purple, Figure 6) associated with C-H bonds [26]; and (c) 288.9 eV (green and blue, Figure 6) for carbon double-bonded to oxygen C=O [22,23]. The P 2p spectrum of the protective film consists of a single component with a binding energy value of 133.41 eV. This indicates that during ATP-6-AHA adsorption on the metal surface, the phosphate atoms are involved in the formation of the protective iron phosphate layer.
The N 1s spectrum observed for the ATP-6-AHA sample at 399.8 eV shows the formation of the covalent N bonds of the organic pigment 6-AHA with carbon and Fe d-metals [26]. The Na + observed for both ATP and ATP-6-AHA at 1071 eV corresponds to the Na + -ions resulting from the sodium chloride electrolyte solution.
Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 8 (~289 eV) (green and blue, Figure 5) correspond to carbon double-bonded oxygen C=O [23]. Moreover, the Na 1s spectrum could be fitted to one component at 1071.1 eV that is related to the presence of Na + -ions [24]. The chemical composition and oxidation states of a low-carbon steel surface with ATP-6-AHA are shown in Figure 6, which demonstrates core level peaks for Fe 2p, O 1s, P 2p, C 1s, and N 1s. The Fe 2p spectrum in Figure 6 shows the respective binding energies of 712 and 719 eV for Fe 2p3/2 and Fe 2p1/2 along with their respective satellite contributions at 719 and 734 eV, which can be assigned to Fe2O3 [21] and FePO4 [20], respectively. The high-resolution spectrum of O 1s exhibits three peaks at 530 (green, Figure 6), 532.5 (brown, Figure 6), and 534 eV (blue, Figure 6). These results clearly demonstrate the presence of Fe2O3 and FePO4, which is in good agreement with Fe 2p3/2 [20]. The O-peak from 6-AHA is likely included in the OH peak at 532.5 eV, as the O 1s peak of organic molecules has been reported to appear at this energy level [25]. The C 1s spectrum contain three components overall: (a) 285.5 eV (brown, Figure 6) corresponding to the covalent C-C bond of the adsorbed organic molecule [25] and carbon adsorbed from contaminants [22]; (b) 286 eV (purple, Figure 6) associated with C-H bonds [26]; and (c) 288.9 eV (green and blue, Figure 6) for carbon double-bonded to oxygen C=O [22,23]. The P 2p spectrum of the protective film consists of a single component with a binding energy value of 133.41 eV. This indicates that during ATP-6-AHA adsorption on the metal surface, the phosphate atoms are involved in the formation of the protective iron phosphate layer.
The N 1s spectrum observed for the ATP-6-AHA sample at 399.8 eV shows the formation of the covalent N bonds of the organic pigment 6-AHA with carbon and Fe dmetals [26]. The Na + observed for both ATP and ATP-6-AHA at 1071 eV corresponds to the Na+-ions resulting from the sodium chloride electrolyte solution. Figure 6. High resolution O 1s, C 1s, Na 1s, Fe 2p, N 1s, Cl 2p, and P 2p XPS peaks obtained from the surface of S235 lowcarbon steel substrate using ATP-6-AHA as an inhibitor after five days of treatment in 3.5% NaCl solution (colors indicate typical bonds, details in the text).

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution:  A non-uniform film covering the S235 steel surface.  Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution: Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 8 (~289 eV) (green and blue, Figure 5) correspond to carbon double-bonded oxygen C=O [23]. Moreover, the Na 1s spectrum could be fitted to one component at 1071.1 eV that is related to the presence of Na + -ions [24]. The chemical composition and oxidation states of a low-carbon steel surface with ATP-6-AHA are shown in Figure 6, which demonstrates core level peaks for Fe 2p, O 1s, P 2p, C 1s, and N 1s. The Fe 2p spectrum in Figure 6 shows the respective binding energies of 712 and 719 eV for Fe 2p3/2 and Fe 2p1/2 along with their respective satellite contributions at 719 and 734 eV, which can be assigned to Fe2O3 [21] and FePO4 [20], respectively. The high-resolution spectrum of O 1s exhibits three peaks at 530 (green, Figure 6), 532.5 (brown, Figure 6), and 534 eV (blue, Figure 6). These results clearly demonstrate the presence of Fe2O3 and FePO4, which is in good agreement with Fe 2p3/2 [20]. The O-peak from 6-AHA is likely included in the OH peak at 532.5 eV, as the O 1s peak of organic molecules has been reported to appear at this energy level [25]. The C 1s spectrum contain three components overall: (a) 285.5 eV (brown, Figure 6) corresponding to the covalent C-C bond of the adsorbed organic molecule [25] and carbon adsorbed from contaminants [22]; (b) 286 eV (purple, Figure 6) associated with C-H bonds [26]; and (c) 288.9 eV (green and blue, Figure 6) for carbon double-bonded to oxygen C=O [22,23]. The P 2p spectrum of the protective film consists of a single component with a binding energy value of 133.41 eV. This indicates that during ATP-6-AHA adsorption on the metal surface, the phosphate atoms are involved in the formation of the protective iron phosphate layer.
The N 1s spectrum observed for the ATP-6-AHA sample at 399.8 eV shows the formation of the covalent N bonds of the organic pigment 6-AHA with carbon and Fe dmetals [26]. The Na + observed for both ATP and ATP-6-AHA at 1071 eV corresponds to the Na+-ions resulting from the sodium chloride electrolyte solution. Figure 6. High resolution O 1s, C 1s, Na 1s, Fe 2p, N 1s, Cl 2p, and P 2p XPS peaks obtained from the surface of S235 lowcarbon steel substrate using ATP-6-AHA as an inhibitor after five days of treatment in 3.5% NaCl solution (colors indicate typical bonds, details in the text).

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution:  A non-uniform film covering the S235 steel surface.  Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].
A non-uniform film covering the S235 steel surface. (~289 eV) (green and blue, Figure 5) correspond to carbon double-bonded oxygen C=O [23]. Moreover, the Na 1s spectrum could be fitted to one component at 1071.1 eV that is related to the presence of Na + -ions [24]. The chemical composition and oxidation states of a low-carbon steel surface with ATP-6-AHA are shown in Figure 6, which demonstrates core level peaks for Fe 2p, O 1s, P 2p, C 1s, and N 1s. The Fe 2p spectrum in Figure 6 shows the respective binding energies of 712 and 719 eV for Fe 2p3/2 and Fe 2p1/2 along with their respective satellite contributions at 719 and 734 eV, which can be assigned to Fe2O3 [21] and FePO4 [20], respectively. The high-resolution spectrum of O 1s exhibits three peaks at 530 (green, Figure 6), 532.5 (brown, Figure 6), and 534 eV (blue, Figure 6). These results clearly demonstrate the presence of Fe2O3 and FePO4, which is in good agreement with Fe 2p3/2 [20]. The O-peak from 6-AHA is likely included in the OH peak at 532.5 eV, as the O 1s peak of organic molecules has been reported to appear at this energy level [25]. The C 1s spectrum contain three components overall: (a) 285.5 eV (brown, Figure 6) corresponding to the covalent C-C bond of the adsorbed organic molecule [25] and carbon adsorbed from contaminants [22]; (b) 286 eV (purple, Figure 6) associated with C-H bonds [26]; and (c) 288.9 eV (green and blue, Figure 6) for carbon double-bonded to oxygen C=O [22,23]. The P 2p spectrum of the protective film consists of a single component with a binding energy value of 133.41 eV. This indicates that during ATP-6-AHA adsorption on the metal surface, the phosphate atoms are involved in the formation of the protective iron phosphate layer.
The N 1s spectrum observed for the ATP-6-AHA sample at 399.8 eV shows the formation of the covalent N bonds of the organic pigment 6-AHA with carbon and Fe dmetals [26]. The Na + observed for both ATP and ATP-6-AHA at 1071 eV corresponds to the Na+-ions resulting from the sodium chloride electrolyte solution. Figure 6. High resolution O 1s, C 1s, Na 1s, Fe 2p, N 1s, Cl 2p, and P 2p XPS peaks obtained from the surface of S235 lowcarbon steel substrate using ATP-6-AHA as an inhibitor after five days of treatment in 3.5% NaCl solution (colors indicate typical bonds, details in the text).

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution:  A non-uniform film covering the S235 steel surface.  Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].
Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].
However, the protective film formed by ATP-6-AHA, as indicated in Figures 7b and 8, is: Figure 6. High resolution O 1s, C 1s, Na 1s, Fe 2p, N 1s, Cl 2p, and P 2p XPS peaks obtained from the surface of S235 lowcarbon steel substrate using ATP-6-AHA as an inhibitor after five days of treatment in 3.5% NaCl solution (colors indicate typical bonds, details in the text).

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution:  A non-uniform film covering the S235 steel surface.  Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].
Slightly denser and more compact. Figure 6. High resolution O 1s, C 1s, Na 1s, Fe 2p, N 1s, Cl 2p, and P 2p XPS peaks obtained from the surface of S235 lowcarbon steel substrate using ATP-6-AHA as an inhibitor after five days of treatment in 3.5% NaCl solution (colors indicate typical bonds, details in the text).

Morphology of Corrosion Products
The SEM micrographs in Figure 7a show the surface of the S235 steel for the blank solution:  A non-uniform film covering the S235 steel surface.  Consists of particles in the form of flowery and sandy platelets, which are the typical shapes of crystallized iron oxides/hydroxides and oxyhydroxide FeO(OH) [27].
It consists rather of broad plates such as crystals with different sizes that are evenly dispersed and a layered region.
Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 9 However, the protective film formed by ATP-6-AHA, as indicated in Figures 7b and  8, is:  Slightly denser and more compact.  It consists rather of broad plates such as crystals with different sizes that are evenly dispersed and a layered region.

Discussion
In the presence of ATP-6-AHA, potentiodynamic polarization results in a 3.5 wt.% NaCl solution, which showed an appreciable decrement in anodic current density ( Table  2). This result suggested that the addition of ATP-6-AHA would reduce the dissolution of the anode and that it would retard the oxygen reaction. Furthermore, the addition of ATP-6-AHA induced a small positive shift of E corr values, which is approximately 70 mV higher than that in blank solution (Table 2).
For a comprehensive investigation on corrosion behavior, EIS was also performed in a 3.5 wt.% NaCl solution. An assessment of the results shows that the addition of ATP-6-AHA increased the polarization resistance Rp by two times compared to the blank solution, which corresponds to an inhibition efficiency of 66%. Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 9 However, the protective film formed by ATP-6-AHA, as indicated in Figures 7b and  8, is:  Slightly denser and more compact.  It consists rather of broad plates such as crystals with different sizes that are evenly dispersed and a layered region.

Discussion
In the presence of ATP-6-AHA, potentiodynamic polarization results in a 3.5 wt.% NaCl solution, which showed an appreciable decrement in anodic current density ( Table  2). This result suggested that the addition of ATP-6-AHA would reduce the dissolution of the anode and that it would retard the oxygen reaction. Furthermore, the addition of ATP-6-AHA induced a small positive shift of E corr values, which is approximately 70 mV higher than that in blank solution (Table 2).
For a comprehensive investigation on corrosion behavior, EIS was also performed in a 3.5 wt.% NaCl solution. An assessment of the results shows that the addition of ATP-6-AHA increased the polarization resistance Rp by two times compared to the blank solution, which corresponds to an inhibition efficiency of 66%.

Discussion
In the presence of ATP-6-AHA, potentiodynamic polarization results in a 3.5 wt.% NaCl solution, which showed an appreciable decrement in anodic current density (Table 2). This result suggested that the addition of ATP-6-AHA would reduce the dissolution of the anode and that it would retard the oxygen reaction. Furthermore, the addition of ATP-6-AHA induced a small positive shift of E corr values, which is approximately 70 mV higher than that in blank solution (Table 2).
For a comprehensive investigation on corrosion behavior, EIS was also performed in a 3.5 wt.% NaCl solution. An assessment of the results shows that the addition of ATP-6-AHA increased the polarization resistance Rp by two times compared to the blank solution, which corresponds to an inhibition efficiency of 66%.
A protective film deposited on the steel surface was detected using XPS and SEM/EDX in the presence of ATP-6-AHA (Figures 6-8).
Through the synergistic effect of ATP and 6-AHA, the performance and corrosion resistance of carbon steel using ATP-6-AHA was improved. Additionally, the shortcomings of the high acidity of aluminum tripolyphosphate that leads to early rusting when used alone can be improved [8,28,29]. The neutralizing substances can regulate the pH of the inhibitor formula [8].
From the XPS and SEM analysis, it was found that the presence of 6-AHA and ATP in the solution creates a synergistic effect for the formation of an iron phosphate film on the steel surface. Consequently, it is possible to propose that the corrosion protection mechanism is associated with the combined efficiency of ATP and 6-AHA and involves several stages, as shown in Figure 9. The 6-AHA enhances the solubility and decreases the acidity of aluminum polyphosphate particles.
Corros. Mater. Degrad. 2021, 2, FOR PEER REVIEW 10 A protective film deposited on the steel surface was detected using XPS and SEM/EDX in the presence of ATP-6-AHA (Figures 6-8).
Through the synergistic effect of ATP and 6-AHA, the performance and corrosion resistance of carbon steel using ATP-6-AHA was improved. Additionally, the shortcomings of the high acidity of aluminum tripolyphosphate that leads to early rusting when used alone can be improved [8,28,29]. The neutralizing substances can regulate the pH of the inhibitor formula [8].
From the XPS and SEM analysis, it was found that the presence of 6-AHA and ATP in the solution creates a synergistic effect for the formation of an iron phosphate film on the steel surface. Consequently, it is possible to propose that the corrosion protection mechanism is associated with the combined efficiency of ATP and 6-AHA and involves several stages, as shown in Figure 9. The 6-AHA enhances the solubility and decreases the acidity of aluminum polyphosphate particles. In the first stage in Figure 9, the decomposition of ATP-6-AHA led to the formation of P 3 O 10 5and H⁺, as indicated in Equation (3). The dissolution of steel takes place, and the iron cations appear, as illustrated in Figure 9. In such acidic conditions, the 6-AHA may also act by decreasing the acidity, conducting the depolymerization of the tri-polyphosphate P 3 O 10 5to PO4 3-orthophosphate particles (Equation (4)).
A protective film of iron phosphate on the steel surface (stage III), as supported by the experimental XPS and SEM findings, may be generated from Equations (5) Through taking advantage of various electrochemical methods, the corrosion inhibition performance of ATP-6-AHA in 3.5% NaCl for S235 low-carbon steel can be defined in this work as the combined effect of phosphate anions, triphosphate anions, and 6-AHA organic molecules that leads to an iron phosphate film that blocks the corrosion sites. Thus, it was evident that both ATP and 6-AHA exhibited a synergistic effect that led to higher resistance. In the first stage in Figure 9, the decomposition of ATP-6-AHA led to the formation of P 3 O 5− 10 and H + , as indicated in Equation (3). The dissolution of steel takes place, and the iron cations appear, as illustrated in Figure 9. In such acidic conditions, the 6-AHA may also act by decreasing the acidity, conducting the depolymerization of the tri-polyphosphate P 3 O 5− 10 to PO 4 3− orthophosphate particles (Equation (4)). A protective film of iron phosphate on the steel surface (stage III), as supported by the experimental XPS and SEM findings, may be generated from Equations (5) Through taking advantage of various electrochemical methods, the corrosion inhibition performance of ATP-6-AHA in 3.5% NaCl for S235 low-carbon steel can be defined in this work as the combined effect of phosphate anions, triphosphate anions, and 6-AHA organic molecules that leads to an iron phosphate film that blocks the corrosion sites. Thus, it was evident that both ATP and 6-AHA exhibited a synergistic effect that led to higher resistance.

Conclusions
The corrosion of low carbon steel is a severe problem in industry. In the present study, the EIS and polarization results in the presence of ATP-6-AHA proved that ATP-6-AHA has a clear inhibitory ability in a 3.5% NaCl solution.
The layered structure of ATP provides a loading ability for 6-AHA as an ecofriendly organic molecule that is able to provide an enhanced corrosion resistance. Nowadays, layered phosphate materials such as ATP exhibit promising potential for the corrosion inhibition of a metal or its alloy. Current research has greatly promoted the application of ATP-6-AHA as an inhibitor in nearly real environments (3.5% NaCl solution). The deintercalation of 6-AHA from the host material was confirmed by means of the XRD and XRF techniques after the electrochemical test. Enhanced efficiency has already been shown to occur with an inhibitor concentration of 0.18 g/L ATP-6-AHA.
In the present work, the inhibition mechanism of ATP-6-AHA was attributed to the synergistic effect of ATP and 6-AHA. The main conclusions can be summarized as follows: • The decomposition of ATP-6-AHA can lead to the formation of P 3 O 5− 10 and H + .

•
The dissolution of steel takes place, and iron cations appear.

•
The formation of the iron phosphate layer on the steel surface was confirmed by the current SEM and XPS analysis.

•
The XPS and SEM analysis for ATP-6-AHA show that all of the P, C, O, and N atoms of the inhibitor are involved in the formation of the protective film, increasing its stability.

Funding:
The financial support of the Materials Science, Energy and Nano-engineering department of Mohammed VI Polytechnic University is acknowledged.

Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.