*2.1. Materials*

Chitosan (low molecular weight) with 85% deacetylation (CS), Lignosulfonic acid sodium salt (LS), MgSO4, sodium citrate, Absolute ethanol, CH3CH2OH (≥99.8%), CaSO4, NH4Cl, NaCl, Na2SO4, KCl, SrCl2, KBr, K2HPO4, HCl, NaOH, hexamethylenetetramine, sodium lactate, and yeas<sup>t</sup> extract were obtained from Sigma-Aldrich (St. Louis, MO, USA). All analytical grade chemicals were used as received. Carbon steel (SS400) rods of 10 mm diameter were obtained locally. The chemical composition of SS400 is 99.25–100% Fe, 0–0.4% Si, 0–0.26% C, 0–0.05% S, and 0–0.04% P. PhenoCureTM (phenolic resin) was procured from Buehler, Lake Bluff, IL, USA.

#### *2.2. Synthesis and Characterization of Cross-Linked CS*/*LS Nanospheres*

CS/LS nanospheres (1:1 CS:LS) were prepared according to our previous work [31]. Briefly, 30 mL of both CS and LS solutions were stirred together at room temperature for 30 min. Then, 450 μL of the cross-linking solution were added gradually, and continued stirring for additional 30 min. The cross-linking agen<sup>t</sup> is a mixture of formaldehyde and sulfuric acid (HCHO/H2SO4, 40/60 *w*/*w*). The resulting solution was purified by centrifuging at 10,000 rpm followed by washing five times with DI water to obtain CS/LS. The size and morphology of the CS/LS were characterized by FEI Quanta 650 FEG SEM (Hillsboro, OR, USA) and FEI Talos F200X TEM (Hillsboro, OR, USA). X-ray diffractogram (XRD) of CS/LS were measured by D8 Advance (Bruker AXS, Bremen, Germany). The X-ray diffractometer is equipped with Cu-Kα radiation (λ = 1.54056 Å) at 40 kV, 40 mA with a step scan of 0.02◦ per step and scanning speed of 1◦ min−1. The hydrodynamic radius and Zeta potential were measured by Malvern Zetasizer Ultra (Malvern Panalytical Ltd., Malvern, UK).

#### *2.3. Fabrication of Coupons and SRB Culture*

The coupons of 8 mm diameter steel bar were fabricated by using SimpliMet 3000 mounting press (Buehler, Lake Bluff, IL, USA) and PhenoCureTM as an outer shell. Then the coupons were polished with EcoMet 2500 Polisher (Buehler, Lake Bluff, IL, USA) in a sequence from 240 to 1200 silicon carbide paper and 6, 3 and 1 μm diamond slurry to ge<sup>t</sup> a mirror-like finish. The coupons were cleaned with acetone and sterilized with absolute ethanol followed by storing the dried coupons in a desiccated environment until further use. The surface roughness was analyzed by KLA P17 stylus profiler (Milpitas, CA, USA) and SEM was used the image the surface morphology.

Mixed SRB culture was enriched from biofilm samples from a local oil field in Qatar as described earlier [24]. The SRB was further cultured in Postage's C medium in a saline media [39,48]. The composition of the inject seawater is given in the Supplementary Table S1. The concentration of SRB biomass was represented by volatile suspended solids (VSS) available in the culture media [24]. The known volume of the SRB biomass were taken and oven dried at inert atmosphere to calculate the VSS. The carbon steel coupons were incubated in 200 mL bottles containing 250 mg VSS/L SRB biomass and were kept shaken at 120 rpm, 37 ◦C. Control experiment was considered as the coupons incubated in a media containing 250 mg VSS/L SRB in the absence of CS/LS. The optimum concentration of CS/LS was directly added to the media in the range of 0–1000 <sup>μ</sup>g·mL−<sup>1</sup> CS/LS and EIS analysis was performed after 10 days of incubation. The *Rct* values from the Nyquist plots were used to evaluate the corrosion inhibition. Next, corrosion inhibition of optimum CS/LS concentration was evaluated at different time intervals (0, 7, 10, 15, 21, 28, and 35 days) [39,49,50]. The abiotic conditions were made by incubating coupons in the SRB-free media at sterile conditions and in absence of CS/LS to differentiate the chemical corrosion [51]. For comparison, 5% glutaraldehyde (GA) was used as a conventional biocide [52,53]. All experiments were performed in an anaerobic chamber at anaerobic conditions. After this, the sealed reaction bottles were kept shaking at different times at 37 ◦C. After particular time intervals, coupons were drawn from the incubation mixture and gently washed with DI water before analysis.

#### *2.4. Electrochemical Measurements*

Electrochemical measurements were recorded by Gamry potentiostat (Ref 600<sup>+</sup>, (Gamry Instruments, Warminster, PA, USA). Treated SS400 carbon-steel coupons were the working electrodes, saturated calomel electrode (SCE) as the reference and graphite disk as the counter electrode. The treated coupons were mounted into a Gamry ParaCell ™ (Gamry Instruments, Warminster, PA, USA) Electrochemical Cell Kit (Part No.992-80) for electrochemical analysis. Simulated inject seawater was used as the electrolyte for all electrochemical experiments. The EIS measurements were recorded over 0.01–10<sup>5</sup> Hz with 10 mV sinusoidal signal. The EIS measurements were performed after achieving the steady-state condition by keeping the setup for 30 min at open circuit potential (OCP). Gamry Echem Analyst software (Version 7.05) (Gamry Instruments, Warminster, PA, USA) was used to analyze the experimental data.

#### *2.5. Biofilm, Corrosion Products, and Coupon Surface Characterization*

For SEM and XPS analysis of SRB biofilm, the incubated coupons were fixed with 2% GA solution for 2 h. After washing the coupons with DI water, dehydration was performed with ethanol, followed by washing with water [39]. The coupons were stored under dry nitrogen before each analysis. The SEM and EDS analyses were performed with FEI Quanta 650 FEG (Hillsboro, OR, USA) SEM after gold (3 nm) coating. XPS analysis was carried out with ESCALAB 250X (Thermo Fisher Scientific, Hillsboro, OR, USA) with AlK α excitation (25 W, hυ = 1486.5 eV) and 1 eV resolution. The X-ray fluorescence (XRF) analysis was carried out with an XGT-7200V X-ray Analytical Microscope (Horiba Scientific, Piscataway, NJ, USA). The X-ray source was operated at 50 kV and 0.8 mA, and generates an X-ray beam from Rh anode that is focused to a spot size of 1.2 mm. To study the post corrosion morphology of carbon steel coupons, biofilms were removed by sonication in ethanol (10 s intervals), 5 mL·L−<sup>1</sup> HCl, and 3.5 <sup>g</sup>·L−<sup>1</sup> hexamethylenetetramine for 5 min followed by drying with nitrogen flow [54]. The post-corrosion morphology of the coupons after 35 days of incubation with and without CS/LS nanospheres were analyzed by SEM and profilometry. In addition, the bare coupon was analyzed for comparison. KLA-Tencor P17 stylus profilometer (Milpitas, CA, USA) at 2 μm resolution, with a loading force of 2 mg was used to capture surface profile images of the coupons. Seven measurements were made at each position on each coupon with a scan size of 400 × 400 μm<sup>2</sup> for each frame. Apex 3d-7 software (Milpitas, CA, USA) was used to calculate the average surface roughness (*Sa*).

#### **3. Results and Discussion**

#### *3.1. Characterization of Cross-Linked CS*/*LS Nanospheres*

The uniform CS/LS nanospheres have been prepared by one-step covalent cross-linking between chitosan (CS) and lignosulfonate (LS) according to our reported method [31]. As shown in the SEM image (Figure 1A), well-dispersed spherical nanoparticles were obtained with an average diameter of 150–200 nm. TEM image further confirmed the well-defined shape of a single CS/LS nanosphere (Figure 1B). CS/LS at 1:1 CS:LS ratio has been considered as optimum ratio for preparing the nanospheres. According to the XRD pattern in Figure 1C, pure CS has two characteristic peaks at 10◦ and 20◦ while LS having a broad peak at 22.6◦ [55–57]. The formation of CS/LS is confirmed by the diminishing of the peak at 10◦, as well as a reduction in intensity, and broadening of the peak at ~20◦. This weaker and broader peak can be attributed to the formation of a new binary framework in which the original structure of both CS and LS can be disrupted. The detailed characterization of this material has been described elsewhere [31]. The average size distribution of CS/LS in the aqueous suspension was stable between 20 and 60 ◦C at pH 3–8 [31]. The stability of CS/LS in simulated seawater was evaluated by measuring the hydrodynamic radius and Zeta potential at varying pH between 3 and 9. The average size of the particles remained within the range of 230–250 nm at acidic media until pH 6. After this pH, the nanospheres have shrunk slightly and remained almost unchanged at pH above 7. This can be attributed to the collapse and deformation of CS/LS at alkaline pH values [31]. As shown in Figure 1D,

the Zeta potential changed to a negative value with point of zero charge at pH 5.8, indicating that the CS/LS nanospheres are negatively charged at neutral pH conditions.

**Figure 1.** (**A**) SEM images of CS/LS nanospheres (Inset shows the size distribution); (**B**) TEM of CS/LS nanospheres (Inset: TEM image of a single nanosphere); (**C**) XRD for CS, LS, CS/LS and (**D**) The size and zeta potential changes with pH of the CS/LS in simulated seawater.

#### *3.2. Investigation of SRB-Induced Corrosion on Carbon Steel*

It is important to investigate the SRB induced MIC in our experimental conditions to make a valid comparison. The SS400 carbon steel coupons were incubated in a solution containing SRB in Postage's C containing simulated seawater. SRB have been enriched from a mixed-culture bacterial sludge obtained from in a real oil filed sample (see experimental section). The coupons were analyzed by EIS after 7, 10, 15, 21, 28, and 35 days of incubation times.

As observed in Figure 2A, the *Rct* values of Nyquist semicircle is higher after 7 days compared to the ones from longer incubation times. A complete biofilm formation is expected to reach the highest protection capacity at 7 days [50,58]. After which, the semicircles diameters gradually decrease with time, indicating a gradual breakdown in the corrosion protection by the biofilm, i.e., faster corrosion rates. A small capacitive semicircle loop appeared at high frequencies, only for 7 days of incubation, mainly due to the precipitation of the corrosion product along with biofilm results in a porous and more adherent outer layer [59]. This high frequency semicircle started to diminish at longer incubation times, and the Nyquist plot behavior is also different compared to the longer incubation times. However, when steady state is reached at around 7 days, mass transfer limitations was dominant over the interfacial activation, which changes the shape of Nyquist from semicircle to a straight line in the low frequency regime.

**Figure 2.** Nyquist (**A**); Bode (**B**,**C**) plots at SRB enriched media. The inset of (**A**) is a magnification of the low impedance region. The EIS were obtained at OCP of 10 mV and sinusoidal signal of 0.01–10<sup>5</sup> Hz. (**D**) Equivalent circuits used to fit the experimental results.

The phase angle, θ, vs. frequency, in logarithmic scale plot (Figure 2B) presents the phase angle peak shifts to lower frequency with the increasing incubation times. The frequency shift confirms the increase in mass or thickness of the corrosion product layer with high electrical capacitance as a result of SRB activity onto carbon steel coupon [58]. Meanwhile, an increase in the capacitance is a result of increases in the mass and thickness of the porous layer, and consequently the surface area. From the impedance modulus |*Z*| vs. frequency, in logarithmic scale plot (Figure 2C), the |*Z*| values at low frequencies are maximum after 7 days, after which it decreases with longer incubation. The higher values of |*Z*| at low frequencies indicating lower corrosion rates [60].

Figure 2D represents the equivalent circuits of the fitted EIS data. *Rs* represents the resistance of electrolyte, *Qf* is the constant phase element (CPE) at the film/solution interface, *Rf* exemplify the pore film resistance, *Qdl* is the CPE of coupon/solution interface, *Rct* is the charge transfer resistance at the coupon/solution interface, and *W* represent Warburg impedance elements. Both circuits have constant phase elements (*Qf*) instead of the ideal electrical double layer capacitors. This was attributed to the surface roughness, inhomogeneous reaction rates distribution, non-uniform thickness, non-uniform composition of the double layer, and/or non-uniform current distribution [61–65]. Since the SRB biofilm provides a more prominent effect during the initial days of incubation, an additional element W is used in the equivalent circuit, corresponding to the diffusion controlled electrochemical process as a result of the complete biofilm formation [59]. As the incubation time increases, the biofilm starts to degrade so the mass transfer is not the controlling factor anymore, so W is removed from the equivalent circuit.

The EIS analysis of the coupons in the abiotic media in the absence CS/LS is shown in Figure S1. The semicircle's behavior is different at 7 and 10 days in the absence of SRB compared to the longer incubation intervals. The precipitation of iron phosphide on the carbon steel surface can be

detected from the change of medium frequency capacitive loops at 15 and 21 days of incubations [66]. Iron phosphide can be homogeneously distributed after precipitating with the ferrous ion produced by the steel dissolution under abiotic conditions [66]. A gradual decrease of the Nyquist plot diameter and the phase peak shift to a lower frequency was observed at a longer incubation time, and confirmed the low corrosion rate in the absence of SRB.

Table 1 gives the *Rct*, as well as *Rf* values of the carbon steel coupons incubated in the presence of SRB after EIS fitting, and Supplementary Table S2 shows the complete EIS fitting data. The *Rct* value is highest at 7 days compared to other incubation times due to maximum protection of the complete biofilm. Afterward, the *Rct* values keep decreasing as the incubation time increases. The decrease in *Rct* value results in an increase in the dissolution kinetics of the metallic surface due to the fast corrosion rates induced by the breakdown of the biofilm that accelerates the corrosion process. Similarly, the *Rf* values are highest at 7 days. The decrease in *Rf* value could be a result of higher porosity of the biofilm on the coupon surface, resulting in the observed accelerated corrosion.


**Table 1.** *Rct*, Rf and IE values after EIS fitting.

#### *3.3. Investigation of CS*/*LS Nanospheres Inhibitory E*ff*ect on SRB Induced Corrosion*

The previous aqueous media analysis indicated that CS/LS-1:1 demonstrates strong inhibition of SRB activities at 100 <sup>μ</sup>g·mL−1. The CS/LS-1:1 demonstrated 48.8% inhibition of sulfate reduction and 54.26% reduction of total organic carbon (TOC) removal [31]. Here, we investigate the ability of the new CS/LS nanospheres to inhibit the biofilm formation and control MIC on the coupon surface. The first step was to identify the optimum concentration of CS/LS that gives maximum corrosion inhibition in a concentration range from 100 to 1000 <sup>μ</sup>g·mL−1. SRB induced corrosion starts progressing after 10 days of incubation. Hence, the impedance analysis was performed after 10 days of incubation [39]. The Nyquist plots are shown in Supplementary Figure S2A and the equivalent circuit used for fitting the impedance plots is shown in Figure 2D. The relation between *Rct* values and CS/LS concentration are given in Supplementary Figure S2B. The *Rct* values of CS/LS are 256, 287, 337, 468 and 307 Ω·cm<sup>2</sup> for 0, 100, 200, 500 and 1000 <sup>μ</sup>g·mL−<sup>1</sup> respectively. From the *Rct* values, it is found that 500 <sup>μ</sup>g·mL−<sup>1</sup> resulted in the maximum corrosion inhibition. At 1000 <sup>μ</sup>g·mL−1, precipitation started to be observed in the reaction medium. Hence, 500 <sup>μ</sup>g·mL−<sup>1</sup> has been selected as the optimum concentrations of CS/LS for further experiments.

The e ffect of incubation time on the carbon steel coupons was investigated by EIS after 7, 10, 15, 21, 28, and 35 days in the media containing SRB at 500 <sup>μ</sup>g·mL−<sup>1</sup> CS/LS. The Nyquist plot (Figure 3A) showed the same trend as in the presence of SRB but the diameter is higher at the corresponding incubation times. The equivalent circuit used is shown in Figure 3D. The increase in the diameter of the semicircle in the impedance spectrum implies corrosion inhibition in the presence of CS/LS. The *Rct* values are 609 and 363.6 Ω·cm<sup>2</sup> respectively (Table 1) for the coupon incubated with and without CS/LS

respectively after 7 days. However, the Nyquist plot behavior is different for 7 days of incubation compared to the longer incubation periods, and there is no high-frequency capacitive loop after 7 days or even at higher incubation times in presence of CS/LS [59,67]. This can be attributed to the formation of CS/LS layer on the metal surface as also confirmed by the increase in *Rf* values.

**Figure 3.** Nyquist (**A**); Bode (**B**,**C**) plots of SRB with CS/LS. The inset is a zoom of the low impedance region. The EIS were recorded at a range of 0.01–10<sup>5</sup> Hz. (**D**) Equivalent circuit used for fitting.

From the phase angle θ vs. frequency, in the logarithmic scale plot (Figure 3B), the phase peak has shifted to a lower frequency with increasing incubation time similar to the SRB corrosion experiments. However, the intensity of the lower frequency shift is less compared to the presence of SRB. Similarly, from the impedance modulus |*Z*| vs. frequency, in logarithmic scale plot (Figure 3C), the |*Z*| value at low frequencies is high in the case of 7 days incubation.

The *Rct* value is maximum at 7 days and it has decreasing with the higher incubation time (Table 1). However, the *Rct* values are about two times more than the SRB corrosion rate at the corresponding incubation intervals and this enhancement in the *Rct* value is due to the corrosion inhibition effect of CS/LS. The inhibitory effect of CS/LS in absence of the SRB is evaluated after 7 days of incubation (Supplementary Figure S3). The CS/LS may compete with the biofilm and form a spatial layer on the coupon surface, and this can be verified by comparing the R*f* values during the initial incubation times [67]. The *Rf* values are 3–3.7 times higher in the presence of CS/LS compared with SRB alone during 7–15 days of incubation. The biofilm breakdown takes place as time lapses, which is confirmed by the decrease in the *Rf*values with longer incubation times.

Corrosion inhibition efficiency (IE) is obtained from:

$$\text{IE} = (R\_{\text{ct}'} - R\_{\text{ct}}) / R\_{\text{ct}'} \tag{1}$$

where *Rct'* is obtained in the presence of SRB with CS/LS and *Rct* is in the presence of SRB alone. The IE at different incubation time intervals is given in Table 1. The maximum corrosion inhibition was found to be 85% in presence of CS/LS. In our previous study, the CZNC inhibitor was able to provide 74% maximum corrosion inhibition with lesser dose of 250 <sup>μ</sup>g·mL−<sup>1</sup> [24]. There was no significant enhancement in the corrosion inhibition, even at the higher dose of 500 <sup>μ</sup>g·mL−1. However, the inhibitor dose of CZNC was limited to 250 <sup>μ</sup>g·mL−<sup>1</sup> due to the ZnO content in the CZNC biocide. Here we were able to use a higher dose of 500 <sup>μ</sup>g·mL−<sup>1</sup> since CS/LS are metal-free and made of renewable components with expected low toxicity. Nevertheless, the toxicity range and environmental impact of the new nanospheres need to be investigated in future studies.

The corrosion inhibition capability of CS/LS has been compared with the commercial GA biocide by EIS analysis. Supplementary Figure S4 shows the Nyquist plots of the coupons incubated in 5% GA after 15 days of incubation showing a lower diameter of the semicircle in the impedance spectrum as compared with CS/LS, which can be attributed to the better corrosion inhibition induced by the CS/LS. The *Rf* and *Rct* values are low (136.4 and 158.8 <sup>Ω</sup>·cm2, respectively) when SRB is incubated with GA as compared with CS/LS (209 and 312.8 <sup>Ω</sup>·cm2, respectively). In the case of SRB with 5% GA, complete bacterial growth can be inhibited; however, a side reaction can be observed between SRB media and GA which is evidenced by the change of media color to pink instead of the expected black (Supplementary Figure S4). Despite the highly efficiency of GA as a biocide, its toxicity effect to the aquatic ecosystems limited their use [6]. Moreover, GA did not entirely suppress the corrosion in the studied medium during longer incubation times, most likely due to the accumulation of some corrosion products in the cracks of the carbon steel surface. Therefore, CS/LS can provide a more benign alternative to minimize or replace the utilization of GA as a biocide.

#### *3.4. Biofilm and Corrosion Products Characterization*

The inhibition of SRB by CS/LS (500 <sup>μ</sup>g·mL−1) and the consequent formation of biofilm and corrosion products on the carbon steel were examined by SEM, EDS, and XPS analysis. Generally, the presence of exopolysaccharides (EPS), which are excreted by the bacteria to adhere to the metal surface, is visible after four days of incubation along with SRB cells (Supplementary Figure S5). In the presence of CS/LS, different morphology of EPS is visible by SEM due to the possible complex formation with the exopolysaccharide component of CS/LS. Few SRB cells are present on the surface but with deformed cell morphology (Figure S5). After 7 days, the adhesion of numerous active SRBs can be seen on the coupon surface (Figure 4A). Meanwhile, the number of attached SRB cells is significantly reduced in presence of CS/LS, even with noticeable damage at the bacterium cell surface (Figure 4B). The CS/LS particles on the metal surface may have hindered the bacterial attachment as indicated by the smaller number of bacteria on the surface. In addition, an obvious damage to the bacterial cell walls can be seen [31]. Similar observations of cell wall damage were observed as the effect of different nanomaterials on other bacteria [28,68]. For example, predominant damage can be induced on most of the SRB cells in presence of 100 <sup>μ</sup>g·mL−<sup>1</sup> of ZnONPs [28]. Another work reported a progressive damage to the cell wall of *Staphylococcus aureus* and *Pseudomonas aeruginosa*, causing a total lysis of cells in contact with the nanocomposites [68]. Chitosan-based CZNC-10 showed a similar behavior on biofilm formation which was attributed to the synergic influence of CZNC-10 bactericidal impact on the SRB together with the formation of a protective coating on the coupon surface [6,24,67].

**Figure 4.** SEM images of the biofilm after 7 days in SRB media (**A**), 21 days (**C**) and 35 days (**E**) of incubations. SEM of the biofilm after 7 (**B**), 21 (**D**) and 35 days (**F**) in SRB media containing 500 <sup>μ</sup>g·mL−<sup>1</sup> CS/LS.

After 21 days, uneven deposits of corrosion products were visible on the coupon surface along with complex porous structure of the biofilm when exposed to SRB alone (Figure 4C) [69]. In the presence of CS/LS, SEM showed different corrosion products and biofilm morphology with few deformed bacteria on the surface (Figure 4D). After 35 days, corrosion products were dominant on the surface along with limited biofilm structures in the case of SRB alone (Figure 4E,F). In the presence of CS/LS, similar observation is present but with different morphology of the corrosion products. No bacteria were visible on the coupon surface in both cases, which could be covered by the corrosion products layer. The different morphology is an implication of heterogeneous corrosion products in presence of the CS/LS nanoparticles. EDS and XRF analysis have quantified the sulfur and iron content in both biofilm and corrosion products. According to the EDS analysis after 35 days, a reduction in the concentration of Fe and S content by 43% and 31% respectively was observed in the presence of CS/LS (Figure S6). The XRF analysis also showed the reduction in Fe and S contents by 56% and 29%, respectively, in the presence of CS/LS, confirming the inhibition of SRB (Supplementary Table S3).

Figure 5 shows the XPS survey of corrosion products after 35 days in SRB media with and without 500 <sup>μ</sup>g·mL−<sup>1</sup> of CS/LS. SRB induced biocorrosion follows the sulfate reduction pathway at the metal surface with the help of a hydrogen intermediate [70]. This sulfide can appear as H2S, HS− ions, S2− ions or metal sulfides, according to the different conditions which build up at the metal surface and

catalyze the corrosion process [71]. As a result, the Fe is oxidized to Fe2<sup>+</sup> and sulfate is reduced to sulfide followed by the formation of FeS. The overall reaction can be written as:

$$4\text{ Fe}^{0} + \text{SO}\_{4}^{2-} + 3\text{ HCO}\_{3}^{-} + 5\text{ H}^{+} \rightarrow \text{FeS} + 3\text{ FeCO}\_{3} + 4\text{ H}\_{2}\text{O}$$

**Figure 5.** XPS survey spectra of the coupon surface incubated in SRB enriched media with and without CS/LS after 35 days incubation.

The peaks of Fe 3p, Fe 2p, C 1s, O 1s, S 2p, and S 2s are observed in both spectra, which can be attributed to corrosion products and biofilm on the coupon. The S 2p and S 2s peaks confirmed the presence of sulfide and organic sulfur which are mainly formed by the SRB activity. However, the smaller peaks of Fe 2p, S 2s and S 2p were observed from coupon incubated with CS/LS. In addition, the high-resolution spectra for Fe 2p and S 2p are examined to confirm the reduction in the intensity of XPS peak as well as to quantify the corrosion products.

The fitted Fe 2p peaks after 35 days with and without CS/LS are shown in Figure 6A,B respectively. Two sharp peaks at 709.6 eV and 707.6 eV (Fe 2p3/2) corresponding to FeO (pink curve) and mackinawite (Fe1<sup>+</sup>xS) (green curve), respectively. Pyrite (FeS2) is present in both spectra (green curve) [50]. In addition, a peek at around 712.4 eV corresponds to Fe3<sup>+</sup> (originated from Fe2O3) is present in both the coupons (black curve) [72]. A sharp peak at around 710.4 eV (Fe 2p3/2) corresponding to FeS (cyan curve) is present in the coupon exposed to SRB alone [73]. The peak at 713.7 eV of (Fe 2p3/2) corresponds to Fe(III)O from Fe2O3 and is found in presence of CS/LS [74]. From the XPS analysis, the corrosion products are mostly FeO, FeS, FeS2, and Fe2O3. However, FeS peak is prominent only in the coupon exposed to SRB alone which confirmed the reduction in SRB activity in the presence of CS/LS.

**Figure 6.** Fitted Fe 2p spectra from coupons incubated in SRB enriched media without CS/LS (**A**) and with 500 <sup>μ</sup>g·mL−<sup>1</sup> CS/LS (**B**) after 35 days of incubation. Fitted curves with different colour correspond to different chemical states; light green corresponds to FeS2 and mackinawite (Fe1 + xS), pink corresponds to FeO, Cyan corresponds to FeS, black and green correspond to Fe2O3.

SEM and surface profilometry were used to analyze the coupon surface after removing biofilms and corrosion products [75–77]. Figure 7 shows the formed pits on the coupon surface. Pits diameter is greater when coupon is incubated in SRB alone as compared with SRB/CS/LS mixture. The widest pit is observed in the coupon incubated with SRB alone is around 8.2 μm diameter while it is only 4 μm in the presence of CS/LS. These results are matching with EIS and XPS data. In addition, the surface roughness of both coupons was also calculated form profilometry. For comparison, the 2D and 3D profilometry images of the bare coupon is shown in Supplementary Figure S7A,B. The average roughness of the bare coupon is 17 ± 2 nm, which is appropriate for bacterial attachment [78–80]. Supplementary Figure S8 displays high-resolution spectra of the coupon surface after removing the corrosion products. After 35 days, the average roughness of the coupons surface was 780 ± 19 nm in the absence of CS/LS inhibitor. While in the presence of CS/LS inhibitor, the average surface roughness is reduced to 458 ± 16 nm, i.e., the surface roughness of the coupon is reduced to approx. 40% in presence of the CS/LS.

**Figure 7.** SEM micrograph of corrosion pits after removing the corrosion products from SS400 coupons incubated in SRB alone (**A**,**B**) and in presence of CS/LS nanospheres (**C**,**D**) after 35 days of incubation.

In general, the corrosion inhibition mechanism of nanomaterials can be originated mainly from their antibacterial effect [6]. The CS/LS antibacterial activity can be explained by their surface charge and active surface of CS and LS [31]. Due to the nanostructure and hydrophilic nature of CS/LS (originated from the presence of large number of amino groups of CS component), CS/LS can readily bind to the negatively charged bacteria, leading to cell membrane disruption [24]. Lignosulfonate component can cause oxidative stress to proteins and DNA in bacteria generated by reactive oxygen species. These two processes can cause a reduction in the cell viability by severe cytoplasmic leakage and loss of cell integrity and EPS contents. Sulfate reduction and co-substrate oxidation assays confirmed the CS/LS inhibitory effect on SRB [31]. The SEM analysis of SRB cells showed cell aggregation and prevalent surface damage after CS/LS exposure [31]. In addition, formation of CS/LS layer on the coupon surface protects the surface from the initial bacterial attachment [81]. Morphological results and EIS experiments sugges<sup>t</sup> that CS/LS have hindered the formation of biofilm and unstable corrosion products on the carbon steel surface.
