The Use of Synthesized CoO/Co3O4 Nanoparticles as A Corrosion Inhibitor of Low-Carbon Steel in 1 M HCl

CoO/Co3O4 nanoparticles (CoO/Co3O4 NPs) were synthesized with egg white. The effectiveness of CoO/Co3O4 NPs to inhibit the corrosion of carbon steel has verified in acidic medium (1 M HCl). It has been found that Langmuir adsorption isotherm is the dominant adsorption process of CoO/Co3O4 NPs on the surface of low-carbon steel. The thermodynamic parameters also demonstrated that the adsorption process of CoO/Co3O4 NPs was a physicochemical, spontaneous, and exothermic process. The electrochemical impedance spectroscopy technique and potentiodynamic polarization were applied. The results obtained in this study showed that CoO/Co3O4 NPs acted as a mixed inhibitor for the anodic reaction and the cathodic reaction, and the efficiency to inhibit the corrosion was 93% at 80 ppm of the inhibitor. The results of scanning electron microscopy (SEM) technique, energy-dispersive X-ray spectroscopy (EDS), and X-ray electron spectroscopy (XPS) confirmed the effectiveness that was obtained using the inhibitor to protect the surface of low carbon steel. Thus, low-carbon steel can be protected against corrosion in acidic medium using CoO/Co3O4 NPs as inhibitors.


Introduction
It is well known that steel is divided into three types depending on the amount of carbon in the metal: low-carbon steel (carbon < 0.3%), medium-carbon steel (carbon from 0.3 to 0.6%), and high-carbon steel (carbon > 0.6%). Low-carbon steel contains a large amount of iron (98% to 99%). Low-carbon steel is often chosen because it is available in most countries, easy to install and weld, so it is used for tasks requiring strength and shaping [1]. It has enough carbon to make it hard and durable, but not brittle.
Therefore, companies prefer to use it in multiple phases (oil-water-gas) to ensure the continuation of the good life for a long time, as many pipelines connect to a single separation facility. This productive technology enables the pipeline to carry oil over a long distance and allows for an easy pipeline change, thus not affecting oil production [2,3]. Low-carbon steel is also used as a basic material for building chemical reactors, and in many industries, such as construction and transportation for its ability to withstand variable temperatures. However, low-carbon steel corrodes spontaneously in the environment due to chemical and electrochemical reactions, especially in acidic solutions [4][5][6].
A hydrochloric acid is the most prevalent stimulation. It corrodes all types of steel and most other alloys. In addition, hydrochloric acid is not an oxidizing agent, therefore, it does not cause passivation on the surface of alloy steels. The concentration of hydrochloric acid is 1M in general practice, since steel is highly reactive with hydrochloric acid, and higher concentrations may cause complete dissolution of the metal. The hydrochloric acid solution (1 M) is used for descaling, acid pickling operations, including hydraulic fracturing, to improve well productivity [7,8], and is used in many factories, petrochemical processes, acidification of oil wells, and to treat rust deposited in metalworking. During the pickling process and acid cleaning, pipe corrosion occurs that cannot and cannot be corrosion experiments were conducted in the absence and presence of the inhibitor at concentrations of 20; 40; 60 and 80 ppm.

Electrochemical Measurements
Electrochemical impedance spectroscopy (EIS) and potentiodynamic polarization measurements were taken using a Gill AC instrument (125 Station Road, Cark, Grange-Over-Sands, Cumbria, United Kingdom. LA11 7NY). Three electrodes, the working electrode (low-carbon steel electrode), counter electrode (graphite electrode), and reference electrode (calomel electrode), used for all measurements. The open-circuit potential measured for 30 min to attain a steady-state. The EIS measurement frequency ranged from 0.01 to 10,000 Hz. Potentiodynamic polarization was applied in a potential range of ±250 mV vs. Eoc at a scan rate of 0.2 mVs −1 .
The low-carbon steel electrode was immersed in 1M HCl in the absence and presence of CoO/Co 3 O 4 NPs (10, 20, 40, 60 and 80 ppm) at 298 and 333 K.
The experiment was repeated three times, and the electrode was re-immersed in the solution for 48 h to ensure the effectiveness of the inhibitor.
The experiment was repeated three times with an error of ±0.05.
The following equations were used to calculate the inhibition efficiency (IE inh (%)):

EIS:
PDP: where R ct and R ct(inh) denote the charge transfer resistance in the absence and presence of the inhibitor, respectively, and I corr and I corr(inh) are the corrosion current densities in the absence and presence of the inhibitor, respectively; these values were calculated from the intersection of the cathodic and anodic Tafel slopes.

The Surface Morphology Study
Scanning electron microscopy (SEM) and energy dispersive spectroscopy (EDS) were conducted with a JSM-6380 LA instrument (JEOL, San Diego, CA, USA) at a high resolution of 3.0 nm and an accelerating voltage of 0.5-30 kV.
X-ray electron spectroscopy was performed to characterize the CS surface by XPS measurements. Measurements were made on SpectrumScan_Qualitative_AlKa.csv, with passing an energy of 20 keV, with a total energy resolution of 1 eV, and an AlKα x-ray source (hν = 1486.6 eV).

Characterization of CoO/Co 3 O 4 NPs
SEM analysis showed the surface morphology of CoO/Co 3 O 4 NPs (Figure 1a,b). Spongy clumps with pores and voids of different sizes are observed; high-contrast light nanoparticles, and cobalt oxides are seen clearly supported on a darker low-contrast porous material which is a carbon byproduct. These features are also clearly seen in lowmagnification images. The particles clump together as spongy islands, which is why they do not appear as spherical as expected [21].

Characterization of CoO/Co3O4 NPs
SEM analysis showed the surface morphology of CoO/Co3O4 NPs (Figure 1a,b). Spongy clumps with pores and voids of different sizes are observed; high-contrast light nanoparticles, and cobalt oxides are seen clearly supported on a darker low-contrast porous material which is a carbon byproduct. These features are also clearly seen in lowmagnification images. The particles clump together as spongy islands, which is why they do not appear as spherical as expected [21].
The analysis of the (TEM) pictures provides us with a clear morphologic characteristic of the synthesized sample as in Figure 1c. The morphology showed homogenous structures with sizes on the nanometer scale. Figure 1d showed the distribution of particles size histogram for the sample which supported that the partials were from 10-20 nm [21]. The CoO/Co3O4 NPs were accurately characterized in the previous study [21]. The EDX analysis was performed to confirm the presence of cobalt oxides, as it appears from the EDX spectrum that the main components of the prepared sample were Co and O elements. CoO/Co3O4 nanoparticles successfully synthesized ( Figure 2) [21].  The analysis of the (TEM) pictures provides us with a clear morphologic characteristic of the synthesized sample as in Figure 1c. The morphology showed homogenous structures with sizes on the nanometer scale. Figure 1d showed the distribution of particles size histogram for the sample which supported that the partials were from 10-20 nm [21].
The CoO/Co 3 O 4 NPs were accurately characterized in the previous study [21]. The EDX analysis was performed to confirm the presence of cobalt oxides, as it appears from the EDX spectrum that the main components of the prepared sample were Co and O elements. CoO/Co 3 O 4 nanoparticles successfully synthesized ( Figure 2) [21]. igure 1. (a,b) SEM image of the as-prepared CoO/Co3O4 NPs with 1000× and 10,000× magnification, (c) TEM image of the as-prepared material, and (d) its histogram for particle size distribution.
The CoO/Co3O4 NPs were accurately characterized in the previous study [21]. The EDX analysis was performed to confirm the presence of cobalt oxides, as it appears from the EDX spectrum that the main components of the prepared sample were Co and O elements. CoO/Co3O4 nanoparticles successfully synthesized ( Figure 2) [21].    [21]. Moreover, these diffraction peaks can be indexed as typical cubic structure for CoO NPs. In this study, no other phases were observed in the XRD patterns, and the carbonaceous byproduct appear as impurities due to the use of egg white in the preparation. XRD pattern indicate the formation of CoO/Co 3 O 4 nanocomposite and most of the peaks present in the XRD belong to Co 3 O 4 phase with fraction of cubic CoO. Figure 4 show the spectrum FTIR of the sample. The result indicates the flowing (i) different bands at (3415, 1650, 1163, 643, 572, and 513 cm −1 ) with fundamental IR active modes in the vibration spectrum, with high frequency bands around 600 cm −1 at tetrahedral (A) site and low frequency bands around 400 cm −1 at octahedral (B) sites. It has been found in other study that the bands at 513 and 643 cm −1 spectrums are correlated with the vibration of Co +3 in octahedral and the Co +2 in tetrahedral hole in the spinel lattice [21]. The appearance of the shoulder band at 572 cm −1 is related to the divalent octahedral metal ion and oxygen ion complex and it could be related to the presence of Co +2 ions at B site. dexing planes (111), (200), (220), (311), and (222) were detected which in agreement with that reported for CoO NPs in other study [21]. Moreover, these diffraction peaks can be indexed as typical cubic structure for CoO NPs. In this study, no other phases were observed in the XRD patterns, and the carbonaceous byproduct appear as impurities due to the use of egg white in the preparation. XRD pattern indicate the formation of CoO/Co3O4 nanocomposite and most of the peaks present in the XRD belong to Co3O4 phase with fraction of cubic CoO.  Figure 4 show the spectrum FTIR of the sample. The result indicates the flowing (i) different bands at (3415, 1650, 1163, 643, 572, and 513 cm −1 ) with fundamental IR active modes in the vibration spectrum, with high frequency bands around 600 cm −1 at tetrahedral (A) site and low frequency bands around 400 cm −1 at octahedral (B) sites. It has been found in other study that the bands at 513 and 643 cm −1 spectrums are correlated with the vibration of Co +3 in octahedral and the Co +2 in tetrahedral hole in the spinel lattice [21]. The appearance of the shoulder band at 572 cm −1 is related to the divalent octahedral metal ion and oxygen ion complex and it could be related to the presence of Co +2 ions at B site.    Figure 4 show the spectrum FTIR of the sample. The result indicates the flowing (i) different bands at (3415, 1650, 1163, 643, 572, and 513 cm −1 ) with fundamental IR active modes in the vibration spectrum, with high frequency bands around 600 cm −1 at tetrahedral (A) site and low frequency bands around 400 cm −1 at octahedral (B) sites. It has been found in other study that the bands at 513 and 643 cm −1 spectrums are correlated with the vibration of Co +3 in octahedral and the Co +2 in tetrahedral hole in the spinel lattice [21]. The appearance of the shoulder band at 572 cm −1 is related to the divalent octahedral metal ion and oxygen ion complex and it could be related to the presence of Co +2 ions at B site.

Mechanism of Adsorption of Inhibitors on Low-Carbon Steel Surface
To guess the mechanism of adsorption of the inhibitor on the surface of the low-carbon steel, the corrosion mechanism of metal dissolution included in the hydrochloric acid solution, and it is known that the anode dissolution of low-carbon steel is [22,23]: The mechanism of the cathode reaction is the evolution of hydrogen: Inhibition of low-carbon steel corrosion in HCl solution is conducted out by adsorption of inhibitor particles, which depend on the chemical components of the inhibitor, the surface nature of the low-carbon steel, the number of active sites and the temperature.
The physical and chemical adsorption process is carried out at the low-carbon steel/ solution interface, by the following methods [4,24]: The electrostatic attraction occurs between the charged metal and the charged damper particles.

2.
A coordinated bond is formed between the free electron pairs in the inhibitor molecules and the vacant d-orbitals of the iron on the metal surface. 3.
The electron donation and electron attraction reaction occur between the inhibitor particles and the metal. 4.
All previous interactions.
Through the results obtained, it is clear that the low-carbon steel surface carries positive charges of Fe 2+ ions that lead to the attraction and accumulation of Clions on the surface, which makes the surface negatively charged, which helps to attract and adsorb CoO/Co 3 O 4 NPs onto the surface of low-carbon steel.
Furthermore, the presence of Co 2+ and Co 3+ in the nanoparticles contribute to the adsorption of the compound on the surface of low-carbon steel by electrostatic interaction and the formation of bridges that bind the Fe 2+ -Cl − -CoO/Co 3 O 4 NPs on the surface ( Figure 5). Likewise, the presence of the free electron pair of donor O atom and the vacant d-orbits of the iron atoms on the surface, form coordinate bonds such as Fe-O-Co that create a layer that protects the surface from continuing corrosion [22,25].

2.
A coordinated bond is formed between the free electron pairs in the inhibitor molecules and the vacant d-orbitals of the iron on the metal surface. 3. The electron donation and electron attraction reaction occur between the inhibitor particles and the metal. 4. All previous interactions.
Through the results obtained, it is clear that the low-carbon steel surface carries positive charges of Fe 2+ ions that lead to the attraction and accumulation of Clions on the surface, which makes the surface negatively charged, which helps to attract and adsorb CoO/Co3O4 NPs onto the surface of low-carbon steel.
Furthermore, the presence of Co 2+ and Co 3+ in the nanoparticles contribute to the adsorption of the compound on the surface of low-carbon steel by electrostatic interaction and the formation of bridges that bind the Fe 2+ -Cl − -CoO/Co3O4 NPs on the surface ( Figure  5). Likewise, the presence of the free electron pair of donor O atom and the vacant d-orbits of the iron atoms on the surface, form coordinate bonds such as Fe-O-Co that create a layer that protects the surface from continuing corrosion [22,25].
The presence of the inhibitor ions (Co 2+ , Co 3+ ) and the O atom enhances the adsorption of the inhibitor on the low-carbon steel surface and forms a protective film, and the decrease in the solubility of cobalt increases the efficiency of the inhibitor.  The presence of the inhibitor ions (Co 2+ , Co 3+ ) and the O atom enhances the adsorption of the inhibitor on the low-carbon steel surface and forms a protective film, and the decrease in the solubility of cobalt increases the efficiency of the inhibitor.

Determination of Thermodynamic Parameters and Adsorption Isotherm
The nanoparticles were adsorbed onto the low-carbon steel surface at the metal/solution interface. Since there are O atoms in the NPs of cobalt oxides, each particle can be considered to have a free electron pair-rich site(s), which can react with iron ions on the surface of the steel. Thus, the nanoparticles are adsorbed on the surface with high efficiency [26].
To describe the adsorption mechanism and find the important parameters that describe the type of interactions occurring between the metal and inhibitor, the Langmuir isotherm model was applied at 298 and 333 K, which is expressed as follows [4,6]: where C inh is the inhibitor concentration and θ is the surface coverage obtained from the EIS measurement, it is calculated using the following equation: where K ads is the adsorption equilibrium constant. C inh /θ vs. C inh plotted as shown in Figure 6. A linear relationship and a correlation coefficient close to 1 (R 2 > 0.999) was obtained ( Figure 6), which means that the adsorption of CoO/Co 3 O 4 NPs onto the lowcarbon steel surface follows the Langmuir adsorption isotherm [27]. The K ads values obtained from the Langmuir isotherm were used to calculate the values of adsorption standard Gibbs free energy (∆G • ads ). The following equations were used to calculate the Gibb's free energy (∆G • ads ), adsorption enthalpy (∆H • ads ), and adsorption entropy (∆S • ads ) of this system [26,28]: where R is the universal gas constant, T (K) is the absolute temperature and 1 × 10 6 ppm is the concentration of adsorbed water molecules.
In general, values of ∆G • ads less than −20 kJ/mol correspond to electrostatic reactions between the inhibitor and the low-carbon steel surface (physisorption). Similarly, values that are lower than −40 kJ/mol involve sharing the charge or transfer from inhibitor to the low-carbon steel surface to form a coordinate bond (chemisorption) [4][5][6].
The nanoparticles were adsorbed onto the low-carbon steel surface at the metal/solution interface. Since there are O atoms in the NPs of cobalt oxides, each particle can be considered to have a free electron pair-rich site(s), which can react with iron ions on the surface of the steel. Thus, the nanoparticles are adsorbed on the surface with high efficiency [26].
To describe the adsorption mechanism and find the important parameters that describe the type of interactions occurring between the metal and inhibitor, the Langmuir isotherm model was applied at 298 and 333 K, which is expressed as follows [4,6]: where Cinh is the inhibitor concentration and θ is the surface coverage obtained from the EIS measurement, it is calculated using the following equation: where Kads is the adsorption equilibrium constant. Cinh/θ vs. Cinh plotted as shown in Figure  6. A linear relationship and a correlation coefficient close to 1 (R 2 > 0.999) was obtained ( Figure 6), which means that the adsorption of CoO/Co3O4 NPs onto the low-carbon steel surface follows the Langmuir adsorption isotherm [27]. The Kads values obtained from the Langmuir isotherm were used to calculate the values of adsorption standard Gibbs free energy (ΔG°ads).
The following equations were used to calculate the Gibb's free energy (ΔG°ads), adsorption enthalpy (ΔH°ads), and adsorption entropy (ΔS°ads) of this system [26,28]: where R is the universal gas constant, T (K) is the absolute temperature and 1 × 10 6 ppm is the concentration of adsorbed water molecules. The thermodynamic parameters listed in Table 1, which shows that the value of ∆G • ads is −32.9 kJ/mol at 298 K, and −33.1 at 333 K, the interaction of the metal surface with the inhibitors is attributed to physical attraction, thus introducing a physisorption adsorption process. In addition to chemical bonding, as CoO/Co 3 O 4 NPs contains many O atoms that have single-pair electrons and π-conjugate electrons, the coordinated interaction can be formed via charge sharing and transfer, thus introducing a chemisorption adsorption process. Therefore, CoO/Co 3 O 4 NPs adsorption on the surface of low-carbon steel surface is a spontaneous physicochemical adsorption process [29,30]. The negative value of ∆H • ads indicates that the adsorption is exothermic, and the positive value of ∆S • ads indicates an increase in randomness due to the competition of nanoparticles ions at the active sites on the low-carbon steel surface [31].
The oxides nanoparticles tend to agglomerate due to strong interparticle magnetic attractions, van der Waals force, and high surface energy [32]. As small nanoparticles rapidly fuse to reach thermodynamic stability and transform into large-sized particles. Thus, the agglomeration process is thermodynamically controlled, and this is evident from the values we obtained in Table 1, that the values of ∆G • ads were almost constant for both temperatures (298, 333 K) [33], as a result of the thermodynamic stability of the protective layer formation from inhibitor particles agglomerated on the surface of low-carbon steel.

Electrochemical Measurements
Electrochemical methods were used to study the concentration effect of the inhibitor on low-carbon steel corrosion in 1 M HCl at 298 and 333 K.

The Electrochemical Impedance Technique
By applying the EIS technique to determine the low-carbon steel's behavior in the absence and presence of an inhibitor (Figure 7) and by comparing the Nyquist diagrams of the low-carbon steel in HCl in the absence and presence of CoO/Co 3 O 4 NPs, it was observed that all the curves followed the same pattern; in this case, the results show a semicircle. The bode and phase angle diagrams showed increased area under the curves in the presence of the inhibitor compared to a blank solution. From the results in Table 2, it noted that the capacity of the double layer decreases and the resistance of the charge transfer increases with increasing concentration of inhibitor, and the inhibition efficiency increased from 59 to 93%. It is noted from Figure 7 that the charge transfer resistance decreases as the temperature increases to 333 K at the same concentration of CoO/Co 3 O 4 NPs. Moreover, the inhibition efficiency decreased for all the inhibitor concentrations with increased the temperature from 298 to 333 K. The equivalent circuit of the results obtained from the electrochemical impedance measurements shown in Figure 8. The results obtained from the EIS technique explained as follows. In the case of the blank solution, the presence of H + ads and Cl − ions in addition to the heterogeneity of the surface causes increased C dl and decreased R ct at the interface of the low-carbon steel surface/HCl solution [17,18]. In the case of the inhibitor, R ct increases and C dl decreases when adding CoO/Co 3  and other complex are difficult to dissolve in an HCl solution [34,35]. Thus, this layer works to cover the exposed area of the electrode surface in the corrosion medium.
Therefore, the corrosion inhibition process is controlled by the adsorption process and not by the diffusion of the nanoparticles on the surface [36,37]. This indicates that the inhibitor acts as a mixed corrosion inhibitor that impedes both the anodic and cathodic reactions by replacing H 2 O molecules with nanoparticles at the interface of the low-carbon steel surface/HCl solution while also adsorbing these nanoparticles to create a protective film on the low-carbon steel surface that protects it from further corrosion [38,39].   The results obtained from the EIS technique explained as follows. In the case of the blank solution, the presence of H + ads and Clions in addition to the heterogeneity of the surface causes increased Cdl and decreased Rct at the interface of the low-carbon steel surface/HCl solution [17,18]. In the case of the inhibitor, Rct increases and Cdl decreases when adding CoO/Co3O4 NPs; additionally, as its concentration increases, the inhibitor particles compete with H2O, Cl -, and H + ads ions for bonding with the Fe 2+ ions on the low-carbon steel surface. The strong layer formed with the [Fe-2Cl-CoO/Co3O4], [Fe-O-CoO/Co3O4] and other complex are difficult to dissolve in an HCl solution [34,35]. Thus, this layer works to cover the exposed area of the electrode surface in the corrosion medium.
Therefore, the corrosion inhibition process is controlled by the adsorption process and not by the diffusion of the nanoparticles on the surface [36,37]. This indicates that the inhibitor acts as a mixed corrosion inhibitor that impedes both the anodic and cathodic reactions by replacing H2O molecules with nanoparticles at the interface of the low-carbon steel surface/HCl solution while also adsorbing these nanoparticles to create a protective film on the low-carbon steel surface that protects it from further corrosion [38,39].

The Potentiodynamic Polarization Technique
PDP curves are plotted for the corrosion of low-carbon steels in the absence and presence of different concentrations of CoO/Co3O4 NPs (Figure 9) at 298 and 333 K, and the curves show a clear displacement in the anode and cathode Tafel slopes with increasing inhibitor concentration. Additionally, the mechanism of the anode and cathode interaction changed, meaning that the inhibitor inhibits both reactions. Therefore, the inhibition efficiency changed from 57 to 94%, when the concentration of inhibitor increased from 10 to 80 ppm, and the inhibition efficiency reached a maximum of 94% at 298 K and 89% at 333 K. The values of the corrosion current density (Icorr), cathodic (βc), and anodic (βa) Tafel slopes and inhibition efficiency (IEinh) were obtained by extrapolating the polarization curve to the IEcorr corrosion voltage and are listed in Table 3.  (Figure 9) at 298 and 333 K, and the curves show a clear displacement in the anode and cathode Tafel slopes with increasing inhibitor concentration. Additionally, the mechanism of the anode and cathode interaction changed, meaning that the inhibitor inhibits both reactions. Therefore, the inhibition efficiency changed from 57 to 94%, when the concentration of inhibitor increased from 10 to 80 ppm, and the inhibition efficiency reached a maximum of 94% at 298 K and 89% at 333 K. The values of the corrosion current density (I corr ), cathodic (β c ), and anodic (β a ) Tafel slopes and inhibition efficiency (IE inh ) were obtained by extrapolating the polarization curve to the IE corr corrosion voltage and are listed in Table 3.    As shown in Table 3, it appears that the corrosion current decreases with an increasing concentration of inhibitor, and the corrosion potential shifts to less negative values. That is, the corrosion potential shifts toward the anode, which means that the presence of the inhibitor inhibits the anodic reaction more than the cathodic reaction [40]. In other words, CoO/Co 3 O 4 NPs act as a mixed type of inhibitor, with the predominant anodic effect. The interaction occurs between the electrons in the inhibitor and the unoccupied d orbital of iron atoms, as well as the donor-acceptor interactions between the lone electron pairs of the O atoms and the vacant d orbital of the steel surface atoms. Where O atoms have single-pair electrons and π-conjugate electrons. In addition, the maximum transformation of E corr is less than 85 mV, which means that CoO/Co 3 O 4 NPs are a mixed-type corrosion inhibitor [41,42]. We also note that the inhibition efficiency of the anodic and cathodic reaction increases with an increasing concentration of inhibitor from 10 to 40 ppm, and after concentration 40 ppm, the increase in efficiency is not noticeable. The increase in the efficiency of the inhibitor with the increase in concentration is due to an increase in the thickness of the layer formed on the surface of the low-carbon steel, which serves to protect the low-carbon steel from continuous corrosion and becomes almost stable at concentrations higher than 40 ppm.
The results of the PDP agreed with those obtained from EIS.

Scanning Electron Microscopy (SEM), Energy-Dispersive X-ray Spectroscopy (EDS) and X-ray Electron Spectroscopy
The surface morphology of low-carbon steel was studied by scanning electron microscopy and energy dispersive spectroscopy after immersion for 30 h in 1 M HCl solution in the absence and presence of 40 ppm of CoO/Co 3 O 4 NPs. Figure 10a shows cracks, pits, and scratches, as well as corrosion deposits on the low-carbon steel surface. From Figure 10b, it can be seen that deposits of CoO/Co 3 O 4 NPs form on the surface, and thus a protective layer is formed on the surface of low-carbon steel. As shown in Figure 10c, the presence of O, Co, and C atoms signals indicate the adsorption of the inhibitor on the surface of low-carbon steel, and its association with the active sites on the metal surface [43]. Furthermore, the multiplicity of the Co atom signals and the decrease in the signals of the Cl atom with the high signal of the Fe atom, indicate the high efficiency of the inhibitor in reducing the corrosion rate and protecting the low-carbon steel surface [22,44].
XPS was performed on the surface of low-carbon steel after being immersed in a 1 M HCl containing 40 ppm of CoO/Co 3 O 4 NPs. The high-resolution C 1s, O 1s, Fe 2p, and Co 2p signals, O 1s dissociation spectrum was obtained in Figure 10d, which can be attributed to the presence of Fe 3+ bound oxides. A spectrum of Fe 2p atom was also observed (Figure 10d) attributed to the presence of ferric ion complexes such as Fe 2 O 3 and/or Fe 3 O 4 [45]. A spectrum of Co 2p atom was also observed (Figure 10d)  XPS was performed on the surface of low-carbon steel after being immersed in a 1 M HCl containing 40 ppm of CoO/Co3O4 NPs. The high-resolution C 1s, O 1s, Fe 2p, and Co 2p signals, O 1s dissociation spectrum was obtained in Figure 10d, which can be attributed to the presence of Fe 3+ bound oxides. A spectrum of Fe 2p atom was also observed ( Figure  10d) attributed to the presence of ferric ion complexes such as Fe2O3 and/or Fe3O4 [45]. A spectrum of Co 2p atom was also observed (Figure 10d) attributed to the presence of cobalt ion complexes such as CoO and/or Co3O4, which form complexes with iron. The XPS results confirm the adsorption of CoO/Co3O4 NPs on the low-carbon steel surface.

Conclusions
The efficacy of CoO/Co 3 O 4 nanoparticles to prevent corrosion of carbon steel in 1 M HCl solution was studied. We will focus on inhibitor concentrations from 10 to 80 ppm for more details in order to find the limit of their effectiveness. When the Langmuir adsorption isotherm model was applied, it was found that the linear relationship was close to unity (R 2 = 0.999), meaning that the inhibitor adsorption process on the low-carbon steel surface followed the Langmuir isotherm. The values of the thermodynamic parameters (∆G • ads , ∆H • ads , and ∆S • ads ) showed that CoO/Co 3 O 4 NPs were spontaneously adsorbed onto the low-carbon steel surface by mixed adsorption (physical and chemical adsorption); additionally, the process was exothermic, and the positive value of entropy was the result of competition between the inhibitor particles at the active sites on the low-carbon steel surface. Electrochemical measurements (EIS and PDP) showed that the inhibition efficiency of the CoO/Co 3 O 4 NPs inhibitor increases with increasing concentration from 10 to 40 ppm. The increase in the efficiency of the inhibitor with increasing concentration is due to the increased thickness of the layer formed on the surface of the low carbon steel, which serves to protect the low carbon steel from continuous corrosion and become almost stable at concentrations above 40 ppm. The CoO/Co 3 O 4 NPs had a high efficiency of 93% at a concentration of 80 ppm and a temperature of 298 K, while the efficiency was 90% at 333 K. The inhibitor acted as a mixed inhibitor that affected both the anodic and cathodic reactions at the interface of the low-carbon steel/HCl solution. Furthermore, the results obtained from SEM and EDS confirmed that the presence of adsorbed deposits on the surface with the appearance of signals for O, Co, and C atoms indicates the adsorption of the inhibitor onto the low-carbon steel surface and its effectiveness in protecting the low-carbon steel surface.