Electrochemical and Computational Analyses of Thiocolchicoside as a New Corrosion Inhibitor for Biomedical Ti6Al4V Alloy in Saline Solution: DFT, NBO, and MD Approaches

Abstract

The Ti6Al4V alloy is considered the most beneficial of the titanium alloys for use in biomedical applications. However, it corrodes when exposed to various biocompatible fluids. This investigation aims to evaluate the corrosion inhibition performance of the Ti6Al4V in a saline solution (SS) using thiocolchicoside (TCC) drug as an environmentally acceptable corrosion inhibitor. The corrosion assessments were conducted using potentiodynamic polarization curves (PPCs), open-circuit potential (OCP), and electrochemical impedance spectroscopy (EIS) methodologies, supplemented by scanning electron microscopy (SEM), energy-dispersive X-ray (EDS) analysis, atomic force microscopy (AFM), and contact angle (CA) measurements. The outcomes indicated that the inhibitory efficacy improved with higher TCC concentrations (achieving 92.40% at 200 mg/L of TCC) and diminished with an increase in solution temperature. TCC’s physical adsorption onto the surface of the Ti6A14V, which adheres to the Langmuir adsorption isotherm, explains its mitigating power. The TCC acts as a mixed-type inhibitor. The adsorption and inhibitory impact of TCC were examined at various temperatures using PPC and EIS. When TCC is present, the corrosion’s apparent activation energy is higher (35.79 kJ mol⁻¹) than when it is absent (14.46 kJ mol⁻¹). In addition, the correlation between the structural properties of thiocolchicoside (TCC) and its corrosion inhibition performance was systematically analyzed. Density Functional Theory (DFT) calculations were utilized to characterize the adsorption mechanism, supported by Natural Bond Orbital (NBO) analysis and Molecular Dynamics (MD) simulations. The combined computational and electrochemical findings confirm that TCC provides effective and enhanced corrosion protection for the Ti6Al4V alloy in a saline environment. These characteristics provide compelling evidence for the suitability of these pharmaceutical compounds as promising corrosion inhibitors.

1. Introduction

The high strength-to-mass ratio and biocompatibility of titanium alloys, which include corrosion resistance, make them desirable alloys [1]. These advantages have led to several applications in biomedical implants, including knee and hip replacements, dental crowns, and skull implants [2,3]. When it comes to titanium alloys for use in biomedical applications, Ti6Al4V is considered the most advantageous [4,5,6]. Furthermore, Ti6Al4V alloy’s extraordinary osseointegration rates, in slight strength-to-mass ratios, and its corrosion resistance have made it useful in orthopedic applications [7,8]. When choosing metallic materials for biological applications, the main considerations are mechanical performance, biocompatibility, tribological properties, and corrosion resistance [9]. To better comprehend biocompatibility and resistance to corrosion under physiological conditions, scientists have closely examined how it behaves in situations that closely resemble the aggressive characteristics of biological fluids. However, the effects of biomolecules on the characteristics of titanium and titanium alloys are poorly understood [10,11,12,13,14]. Several authors have demonstrated that Ti and its alloys corrode when subjected to various biocompatible fluids, including Ringer’s solution, NaCl, and artificial saliva [15,16]. A surface oxide film may have an absorbent external layer and a dense inner layer, depending on the circumstances. The primary factors influencing titanium implant biocompatibility are the oxide layer’s electrochemical properties and its long-term resilience in biological settings [17,18,19,20,21,22]. Proteins and amino acids, as biomolecules, can stick to metallic exteriors and function as ligands, forming metal complexes on the metal surface that might slow down corrosion processes [23]. There are numerous varieties of corrosion inhibitors, and each one functions differently and has a different chemical makeup. Despite being used as metal corrosion inhibitors, inorganic corrosion inhibitors like phosphates and chromates have several drawbacks, chief among them being their toxicity. Organic corrosion inhibitors containing heteroatoms of nitrogen, oxygen, and sulfur, conjugate π-bonds, and aromatic rings in a chemical construction exhibit notable inhibitory activity [24,25]. Metal corrosion is considerably reduced by the adsorption of corrosion inhibitor particles on the metallic surface. Their chemical and structural properties affect how well corrosion inhibitors work [26,27]. All of these corrosion inhibitors are hazardous, and their manufacture is expensive and difficult [28,29]. When these corrosion inhibitors are released into the soil and water, they build up and cause environmental problems. It is also necessary to add organic solvents to dissolve these inhibitors in the medium, which exacerbates the pollution problems in the environment.

Many medications, including antibiotics and other medications, effectively stop corrosion [30,31]. In this drug-based corrosion inhibitor, cyclic organic molecules with rings of five or six members are present. Nitrogen, sulfur, and oxygen are found in the basic five-membered heterocycles pyrrole, thiophene, and furan, respectively. The rings have six members, including pyridine, pyrimidine, and triazines. Pyrazoles, imidazoles, oxazoles, thiazoles, thiadiazoles, pyrazines, and pyrimidines are examples of corrosion-inhibiting compounds that can be made by substituting nitrogen or other elements for more than one carbon atom. It is important to keep in mind that these elementary constructions are insufficient to stop corrosion on their own. Thus, more heterocycles, phenyl rings, π-bonds, and useful groups must be added to these molecules to modify them further. Many drugs have gotten too much attention in recent years [32,33,34,35,36]. In comparison to the more conventional corrosion inhibitors based on heterocyclic molecules, this method of drug use is realistic, cost-effective, and time-efficient [37]. A muscle relaxant with analgesic and anti-inflammatory properties, thiocolchicoside (TCC) is the drug most frequently recommended to treat sudden, painful muscle spasms [38,39,40]. Easy solubility in water, low cost, non-toxicity, and the existence of seven-membered rings that facilitate adsorption are some of TCC’s benefits as a safe corrosion inhibitor.

To our knowledge, no information has been published in the literature about thiocolchicoside’s (TCC) ability to suppress corrosion of Ti6A14V alloy or any other metal.

This study thus documents, for the first time, the thiocolchicoside (TCC) inhibitory activity of Ti6A14V alloy in a saline solution (SS). The corrosion behavior of the Ti6A14V alloy in an SS is assessed in this work using EIS, OCP, and PPCs in combination with SEM/EDS, AFM, and CA probes. Moreover, the structural properties and adsorption performance of TCC were examined theoretically using density functional theory (DFT), natural bond orbital (NBO) analysis, and molecular dynamics simulation (MD) techniques to investigate their inhibition effectiveness. These findings lay the groundwork for a comprehensive understanding of Ti alloy corrosion in biomedical settings, with exceptional corrosion resistance for use in biomedical applications.

2. Materials and Methods

2.1. Sample Preparation

The Ti6Al4V alloy samples were provided by Japan Coating Co., Ltd. (Tokyo, Japan). The chemical composition of the Ti6Al4V alloy is reported elsewhere [30]. The alloys were mounted in epoxy cold resin, exposing a 1.0 cm² surface area to the saline solution (SS). Before testing, the electrode surfaces were sequentially polished with silicon carbide sandpapers of grades 500, 800, and 1200, followed by rinsing with distilled water and acetone. The electrodes were then activated by immersion in 1.0 M hydrogen fluoride for 1 min and subsequently rinsed with double-distilled water.

A saline solution (0.9% NaCl, pH 5.0) was prepared using deionized water and analytical-grade reagents for all experiments. TCC was obtained from an Egyptian pharmacy (Figure 1). The TCC solution was prepared by dissolving five tablets (4 mg each) in 100 mL of deionized water, followed by dilution with 0.9% NaCl to achieve the desired concentration.

2.2. Electrochemical Testing

Electrochemical measurements were conducted using a Gamry Instrument Potentiostat/Galvanostat/ZRA (Model 1000) Warminster, Pennsylvania, USA. The Ti6Al4V alloy served as the working electrode, platinum as the auxiliary electrode, and Ag/AgCl as the reference electrode.

Potentiodynamic polarization curves (PPCs) were recorded at a sweep rate of 2 mV s⁻¹ with a potential range of −0.6 to +0.2 V. Electrochemical impedance spectroscopy (EIS) measurements were performed over a frequency range of 100 kHz to 10 mHz, with an AC amplitude of 5 mV (peak-to-peak). Each experiment was conducted in triplicate to ensure reproducibility. The corrosion susceptibility of the Ti6Al4V micro-implant was assessed based on the obtained electrochemical data, following established test methodologies.

2.3. Surface Characterization

After electrochemical testing, the surface morphology of the Ti6Al4V samples was examined using a JEOL JEM-1200EX II scanning electron microscope (SEM). Atomic force microscopy (AFM) and Raman spectroscopy were performed using a WiTec Alpha 300R Raman Imaging Microscope. AFM images were obtained in non-contact mode using a silicon cantilever (resonance frequency: 280–300 kHz; force constant: 42 N/m).

The wettability and hydrophobicity of the metal surfaces were evaluated through contact angle (CA) measurements using a Model DSA258 goniometer (KRUSS GmbH, Hamburg, Germany).

2.4. Computational Studies

2.4.1. Quantum Theoretical Computations

The various molecular parameters of TCC are determined using Gaussian View 5.0.9 by visualizing the simulation of the structural features and the vibrational frequencies. Becke’s theoretical calculations, which depend on DFT, are performed using Lee–Yang–Parr (B3LYP) three-parameter function with a 6–311++ G (d,p) basis set by using the Gaussian 09 program package [41]. The global reactivity determined by DFT which applied to, calculate the E_HOMO of the highest occupied energies, and lowest unoccupied molecular orbital E_LUMO, gap energy (ΔE), moment dipole (μ), ionization (I) energy, electron affinity (Y), absolute (ϕ) electronegativity, (ψ)absolute hardness, (S) absolute softness, global electrophilicity (ω), nucleophilicity (ε), power electro-accepting (ω+), power electro-donating (ω−), the donation back ΔE, fraction transferred electrons (ΔN) and energy inhibitors interaction (ΔE_TiAlV/TCC). Utilizing Fukui functions, which are used to analyze the local reactivity of the studied inhibitor molecules [42,43,44]. The orbital interactions, atomic charges, and their effects on the structure and stability of the examined structures were calculated using the natural bond orbital (NBO) approach.

2.4.2. Molecular Simulation Dynamics

The TCC inhibitor is adsorbed on the surface by Molecular Dynamics Simulation (MD). The TCC and the Ti6Al4V surface interaction were examined in an interacting system without any molecular solvent [45]. Dimensions with a simulation box of 24.32 Å × 24.32 Å × 9.10 Å were performed to model the descriptive part; periodic boundary conditions and the interface free of capricious boundary impacts were applied. Initially, the construction and relaxation of the Ti alloy surface with higher periodicity and surface area are used as a supercell. Finally, the Ti alloy surface has a thickness of 30 Å for a vacuum slab capable of learning the TCC that interacts with the Ti alloy surface. In the calculation used the non-bond cutoff structure’s layers were used. The TCC inhibitor compound could interact with ten surface layers of Ti alloy atoms in non-bonding interactions without requiring excessive computation time. Afterwards, the structure was converted to 3D periodicity. The Dynamics Discover molecular module investigates thermodynamic parameters such as time simulation, temperature, and pressure, as well as the initiation of dynamic computation procedures for performing molecular dynamics simulations [46,47,48].

2.4.3. NBO Analysis

Natural Bond Orbital (NBO) analysis originated as a technique for studying hybridization and covalence effects in polyatomic wave functions that particularly exhibited hydrogen-bonded and other strongly bound van der Waals complexes [49]. The covalence effects in molecules are described by the filled NBOs σ of the ‘‘natural Lewis’s structure’’ [50]. However, the non-covalent effects were described by the general transformation to NBOs that leads to orbitals that are unoccupied in the formal Lewis structure. The symbols σ and σ* are used in a generic sense to refer to occupied and unoccupied orbitals of the formal Lewis structure, though the former orbitals may be core orbital’s (CR), lone pairs (LP), σ or π bonds (σ, π), and so forth, and the latter may be σ or π antibound (σ*, π*), or extra valence shell Rydberg (RY*) orbitals.

The NBO analysis reveals intra- and intermolecular interactions between donor and acceptor orbitals, specifically between filled (Lewis-type and bonding) and empty (non-Lewis or antibonding) natural bond orbitals. The stabilization energies of these interactions are estimated using second-order perturbation theory [49]. According to the equation below, the stabilization energy E⁽²⁾ [50] associated with electron delocalization between the donor NBO (i) of electrons and the acceptor NBO (j) of electrons is calculated following Equation (1):

E⁽²⁾ = ΔEij = qi (F (ij) 2/εj − εi),

(1)

Fijis (ij) is an element of the off-diagonal NBO Fock matrix, qi represents the occupation of the donor orbital, εi and εj are the energies of the diagonal elements of NBOs of the acceptor and the donor, respectively.

3. Results and Discussion

3.1. TCC as an Efficient Inhibitor for Ti6Al4V Alloy

3.1.1. PPCs

The influence of TCC on the corrosion characteristics of the Ti alloy in an SS was examined through the polarization technique. Figure 2 examines the Tafel PPCs of the Ti alloy following a 1 h immersion in an SS with different concentrations of TCC (40–200 mg/L) at 310 K. Potentiodynamic variables derived from Tafel plots contain corrosion potential (E_corr), corrosion current (I_corr), and cathodic and anodic Tafel slopes (βc and βa). Figure 2 and

Table 1. Tafel parameters obtained for a Ti6Al4V alloy in an SS with different concentrations of TCC at 310 K.

[TCC] mg/L	ICorr A cm−2	−ECorr /V	βa (V dec−1)	βc (V dec−1)	CR Mpy	$\mathsf{\Theta }$	ղPol (%)
0.0	3.08 × 10−6	0.297 ± 0.04	0.210 ± 0.03	0.294 ± 0.03	0.396 ± 0.07	-	-
40	1.46 × 10−6	0.255 ± 0.03	0.656 ± 0.04	0.238 ± 0.04	0.188 ± 0.04	0.525 ± 0.05	52.50 ± 3
80	9.10 × 10−7	0.226 ± 0.02	0.128 ± 0.02	0.108 ± 0.06	0.117 ± 0.03	0.704 ± 0.03	70.40 ± 2.5
120	5.51 × 10−7	0.189 ± 0.02	0.077 ± 0.05	0.067 ± 0.04	0.070 ± 0.02	0.821 ± 0.04	82.10 ± 2.0
200	2.32 × 10−7	0.170 ± 0.02	0.035 ± 0.06	0.050 ± 0.03	0.029 ± 0.02	0.924 ± 0.02	92.40 ± 1.5

show that the addition of TCC under investigation results in a reduction in both I_corr and the rate of corrosion (CR). This decreasing effect is enhanced by raising the TCC concentrations. For example, I_corr dropped from 3.08 × 10⁻⁶ A cm⁻² (without TCC) to 2.32 × 10⁻⁷ A cm⁻² (with 200 mg/l of TCC). In addition, the CR was lowered by 13.5 times when 200 mg/l of the TCC inhibitor was present (Table 1). The high βa value at 40 mg/L is not an unusual case but instead reflects specific surface behavior under partial inhibition conditions, where the non-uniform adsorption affects electrochemical kinetics, and it may interfere with passive film behavior.

Furthermore, when TCC concentration increased, the corrosion potential (E_corr) value demonstrated a discernible shift toward more noble potentials. TCC appears to be a mixed-type inhibitor that influences both anodic and cathodic polarization. The following relationship was used to calculate the inhibition effectiveness, ղ_Pol (%), from the measured I_corr values [47]:

$${\mathrm{ղ}}_{\mathrm{Pol}} (\%) =\mathsf{\theta }\times 100={\displaystyle \frac{\mathrm{I}\mathrm{c}\mathrm{o}\mathrm{r}\mathrm{r}-\mathrm{I}\mathrm{c}\mathrm{o}\mathrm{r}\mathrm{r}\left(\mathrm{i}\mathrm{n}\mathrm{h}\right)}{\mathrm{I}\mathrm{c}\mathrm{o}\mathrm{r}\mathrm{r}}}\times 100$$

(2)

While θ represents the surface covering, I_corr and I_corr(inh) stand for the corrosion current without and with varying TCC concentrations, respectively. Higher TCC concentrations lead to higher η_pol%. For instance, at a small amount of TCC (40 mg/L), the η_Pol% reaches 52.50%; however, at a higher concentration (200 mg/L), it achieves 92.40%. The results imply that TCC molecules are adsorbed at the interface between the Ti6Al4V alloy and the solution, creating an insulating film that shields the electrode surface and partially blocks the active sites of the corrodent. When the TCC concentration rises, more TCC molecules adsorb on the surface of the alloy, increasing its coverage. This is illustrated by the increase in η_pol% with higher inhibitor dosages. The surface coverage, for example, rises from 0.525 (at 40 mg/L of TCC) to 0.924 (at 200 mg/L). The TCC monolayer acts as an efficient protective film, suppressing both the oxidation and reduction processes, as demonstrated by the changes in (βa) and (βc) as the inhibitor’s concentration increases.

3.1.2. Impedance Analysis

EIS was employed to analyze the alterations in the protective barrier/SS interface that transpired when the Ti6Al4V alloy samples were exposed to an SS having different concentrations of TCC. A single, extremely polarization-resistant capacitive loop was observed in SS Nyquist plots (Figure 3a) with the addition of TCC. The increased number of adsorbed molecules on the surface of the Ti6Al4V alloy and the improved surface coverage of TCC on the Ti6Al4V alloy due to the adsorption process are the reasons why a study of the Nyquist drawing reveals that the circumference of the half-circle enhances when TCC is present.

Figure 3b depicts the impedance curves and corresponding phase angle versus frequency. The addition of the corrosion inhibitor increases the phase angle and the absolute impedance value. The adsorption and inhibition are supported by the increase in log |Z| values that occurs when the TCC inhibitor is introduced to the SS. These findings corroborate the enhanced capacitive functioning of the adsorbed TCC film at the interface between the Ti alloy and SS [51,52]. This demonstrates how TCC is adsorbed and how the TCC-Ti alloy is shielded by the development of a protective layer. High protective effectiveness and a reduction in the TCC-Ti alloy’s corrosion rate at higher frequencies are indicated by a shift in phase angle towards 90 degrees as TCC concentration rises [53,54]. The increased phase angle values for the inhibited samples demonstrated the protective layer of inhibitors covering the Ti alloy surface. The increase in width and move to minimal frequencies of the single maximum in the Bode graphs lends support to the theory that inhibitor molecules form protective coatings [55,56].

As demonstrated in Figure 4, the obtained EIS data is fitted employing a two-time constant equivalent circuit (EC) [57]. The chi-square value (χ²) (

Table 2. Fitting parameters of EIS obtained for a Ti6Al4V alloy in an SS with different concentrations of TCC at 310 K.

Concentration mg/L	Rs (Ω cm2)	Rct (kΩ cm2)	Qdl (F cm2 HZ1−n1)	Rf (KΩ cm2)	Qf (F cm2 HZ1−n2)	Rp (Rf + Rct) (kΩ cm2)	χ2 ×10−9	$\mathsf{\Theta }$	ղEIS (%)
0.0	16.79 ± 0.67	7.80 ± 0.55	79.61 × 10−6	0.045 ± 0.005	197.0 × 10−6	7.85 ± 0.55	0.227	-	-
40	18.30 ± 0.73	21.77 ± 1.5	59.02 × 10−6	0.067 ± 0.007	182.9 × 10−6	21.83 ± 1.5	0.552	0.641	64.1 ± 3
80	20.83 ± 0.83	25.01 ± 1.8	47.54 × 10−6	0.073 ± 0.007	166.2 × 10−6	25.08 ± 1.8	0.027	0.688	68.8 ± 3
120	33.25 ± 1.7	47.12 ± 3.3	33.29 × 10−6	0.088 ± 0.009	140.3 × 10−6	47.20 ± 3.3	0.732	0.834	83.4 ± 2.5
200	55.53 ± 2.8	78.79 ± 5.5	22.64 × 10−6	0.096 ± 0.010	77.60 × 10−6	78.88 ± 5.5	0.856	0.901	90.1 ± 2.0

) illustrates the discrepancy between the modeled data and the observed value of impedance analysis; a smaller chi-square value denotes less variance. The EC is composed of the constant phase elements (Q_f and Q_dl), which include the film capacitance (C_f) and double-layer capacitance (C_dl), the electrolyte resistance (Rs), the charge transfer resistance (R_ct), and the resistance of the film formed on the Ti alloy surface (R_f) EC [58].

When an ideal capacitor is not suitable for the corroded Ti alloy electrode, a constant phase element (CPE, Q) is employed to substitute capacitance C because of the heterogeneity of the Ti alloy surface following corrosion in the medium. The following Equation (3) defines the CPE impedance [58]:

Z_CPE = Q⁻¹(iω)⁻ⁿ

(3)

The angular frequency ω = 2πf, the CPE exponent, which has assessments extending from −1 to 1, and an imaginary number with i² equal to −1 are the parameters (i, ω, n) in that order. It is crucial to keep in mind that the arbitrary value of n has a specific relevance when characterizing the circuit elements identified by CPE. Additionally, the CPE and the double layer’s capacity (C_dl) have the following relationship [59]:

$$C_{dl}=\sqrt[n]{Q· {R_p}^{1-n}}$$

(4)

Data on several electrochemical parameters, including phase shift (n), double-layer capacitance (C_dl), polarization resistance (R_P), solution resistance (R_S), and Q_CPE constant, are shown in Table 2. The Rp, which is the addition of R_f and R_ct, can be applied to assess a material’s capability to resist corrosion in corrosive environments. The correlation between the corrosion rate and the Rp is inverse [59]. Table 2 shows the fitting data for the TCC inhibitor at different doses that were obtained from the EIS diagrams. As shown in this table, the Q_dl values of TCC and the blank system differ significantly. The drop in Q_dl is usually caused by the TCC molecules’ propensity to stick to the Ti alloy surface, emphasizing the role of molecular adsorption in preventing corrosion [60].

As a result, the lower Q_dl indicates the TCC protective film’s superior barrier function. On the other hand, when TCC is present at 200 mg/L, the polarization resistance (R_P) rises from 7.85 kΩ cm² for the blank solution to 78.88 kΩ cm². This implies that the adsorbed TCC barrier layer on the electrode surface has thickened. TCC provides the best protection because it adsorbs on the Ti6Al4V alloy surface. The inhibitory efficiency in Table 2 is estimated and reported employing the following formula [61]:

$$\mathrm{ղ}\mathrm{E}\mathrm{I}\mathrm{S}\left(\%\right)= {\displaystyle \frac{\mathrm{R}\mathrm{c}\mathrm{t}-\mathrm{R}°ct}{\mathrm{R}\mathrm{c}\mathrm{t}}}\times 100$$

(5)

where R_ct and R°_ct stand for charge transfer resistances in the presence and absence of TCC inhibitors, respectively. The electrochemical variables R_s and R_ct, which were determined using impedance fitting, and the estimated values Q_dl and $\mathrm{ղ}\mathrm{E}\mathrm{I}\mathrm{S}$ (%), are recorded in Table 2. The results demonstrate that the effectiveness of inhibition went up from 64.1 to 90.1% as the TCC concentration was increased from 40 to 200 mg/L. Table 2 shows that R_ct increases significantly as TCC concentration increases, while Q_dl decreases. A high R_ct indicates a slow-corroding system. Furthermore, enhanced inhibitor protection has been linked with a reduction in metal capacitance. The TCC functioned through adsorption at the Ti alloy/SS interface, as evidenced by the reduction in Q_dl caused by a rise in the thickness of the electrical double layer and a decline in the limited dielectric constant.

3.1.3. OCP Measurements

The effects of varying TCC inhibitor doses (40–200 mg/L) at 310 K on the OCP values of the Ti6Al4V alloy concerning dipping period in an SS are examined, with findings presented in Figure 5. For the development of barriers on the Ti6Al4V alloy surface, the corrosion potential progressively increased to more noble potential values before reaching steady-state potential values (after 300 s) at approximately, −0.354, −0.344, −0.328, −0.275, and −0.241V, which correspond to 0, 40, 80, 120, and 200 mg/l of TCC inhibitor concentration, respectively. The steady-state potentials produced indicated improved surface film stability. The potential shifts toward a more noble direction as TCC concentration in the SS goes up, enhancing the film thickness and further isolating the base metal from the SS. This characteristic accelerates the production of protective layers, which prevent Ti6Al4V alloys from disintegrating and reduce corrosion.

3.2. The Impact of Temperature and Thermodynamic Investigations

3.2.1. PPCs

PPCs measurements for the Ti6Al4V alloy under investigation in an SS, both with and without TCC, were tested at temperatures extending from 310 to 340 K to give detailed knowledge about the kind of inhibitor adsorption and its efficiency.

Table 3. Tafel kinetic parameters obtained for a Ti6Al4V alloy in an SS with and without the TCC at different solution temperatures.

Temperature K	ICorr A cm−2	−ECorr /V	βa (V dec−1)	βc (V dec−1)	Corr Rate mpy	Θ	ηpol%
0.00 mg/L
310	3.08 × 10−6	0.297	0.110	0.094	0.396	-	-
320	5.29 × 10−6	0.334	0.313	0.262	0.681	-	-
330	8.50 × 10−6	0.345	0.221	0.120	1.098	-	-
340	1.22 × 10−5	0.362	0.425	0.238	1.574	-	-
200 mg/L
310	2.32 × 10−7	0.170	0.035	0.050	0.029	0.924	92.4
320	1.00 × 10−6	0.223	0.144	0.154	0.084	0.825	82.5
330	2.96 × 10−6	0.261	0.219	0.175	0.380	0.651	65.1
340	7.09 × 10−6	0.333	0.518	0.314	0.913	0.418	41.8

and Figure 6a,b show that the temperature raised the I_corr and the CR regardless of the existence of TCC.

In the absence of TCC, the E_corr values moved from −0.297 V to −0.362 V as temperature increased from 310 to 340 K. On the other hand, the inclusion of the TCC in the SS moved the potential to more negative values (from −0.170 V to −0.333 V). As the temperature increased, the E_corr values shifted to a higher cathodic potential.

These results also demonstrate that both the anodic and the cathodic reactions speed up as a result of increasing the temperature [62,63]. Therefore, as the temperature rises, corrosion visibly increases. The slopes of the βc and βa Tafel lines remain consistent as temperature increases. This reveals that whilst the corrosion mechanism is unaffected by temperature, the alloy surface begins to corrode. The findings showed that as the temperature rises, the inhibition efficiency descends. For instance, Table 3 illustrates the correlation between the TCC concentration and the Ti6Al4V alloy’s efficiency of inhibition (η_pol%) at different temperatures. The observed behavior could be attributed to the inhibitor molecules being physically adsorbed, as higher temperatures may impair the adsorption process. As a result of the inhibitor adsorption and formation of a physical barrier on the alloy surface, a lowering in the alloy’s reactivity in electrochemical processes occurs.

The Arrhenius Equation (6) and the transition state Equation (7) can be utilized properly to understand this phenomenon [64]:

$$\mathrm{L}\mathrm{o}\mathrm{g}\mathrm{I}\mathrm{c}\mathrm{o}\mathrm{r}\mathrm{r}={\displaystyle \frac{-\mathrm{E}\mathrm{a}}{2.303\mathrm{R}\mathrm{T}}}+\log \mathrm{A}$$

(6)

$$\mathrm{L}\mathrm{o}\mathrm{g}{\displaystyle \frac{\mathrm{I}\mathrm{c}\mathrm{o}\mathrm{r}\mathrm{r}}{T}}=\mathrm{L}\mathrm{o}\mathrm{g}{\displaystyle \frac{\mathrm{R}}{Nh}}+{\displaystyle \frac{\Delta Sa}{2.303R}}-{\displaystyle \frac{\Delta Ha}{2.303RT}}$$

(7)

Pre-exponential factor is denoted by A, Planck’s constant (6.626176 × 10⁻³⁴ Js) by h, Avogadro’s number (6.022 × 10²³ mol⁻¹), entropy and enthalpy of activation by ΔS_a and ΔH_a, and the corrosion process’s activation energy by E_a. These equations are drawn as log I_corr and log (I_corr/T) versus the reciprocal of temperature, respectively, in Figure 7. The slopes and intercepts of these equations can be employed to assess the thermodynamic factors. The activation energy E_a and the constant A were calculated using the slope (−E_a/2.303R) and intercept (log A) of Equation (6), respectively. The values of ΔH_a and ΔS_a were calculated using the slope (−ΔH_a/2.303 R) and an intercept [(log (R/Nh) + (ΔS_a/2.303 R)] of Equation (7), respectively. The assembled data is shown in

Table 4. Thermodynamic parameters in the presence and absence of TCC in an SS.

Solution	$\Delta \mathit{H}\mathit{a}$ (kJ mol−1)	$\Delta \mathit{S}\mathit{a}$(J mol−1 K−1)	Ea (kJ mol−1)
Without TCC	13.59	−64.57	14.46
With 200 mg/L TCC	34.56	−33.62	35.79

. The TCC’s adsorption on the surface of the Ti6Al4V alloy is essential to the protective mechanism. The TCC molecules may be adsorbed chemically or physically onto the Ti alloy surface. E_a ranges from 40 to 80 kJ mol⁻¹ for chemical adsorption and from 5.0 to 40 kJ mol⁻¹ for physisorption. Because the E_a value is higher when TCC is present than when it is not, the results imply that the inclusion of the examined TCC decreases the dissolution rate of the Ti6Al4V alloy. Consequently, TCC may be a potent inhibitor in an SS to stop aggressive Ti6Al4V alloy corrosion. Considering that E_a is increased by the addition of TCC to the SS, and that the magnitude of the enhancement varies with the inhibitor concentration.

The mechanism of adsorption on Ti6Al4V in an SS, including an inhibitor, was within the physical one (E_a = 35.79 kJ mol⁻¹) (Table 4). Positive ΔHa values indicate endothermic dissolution in Ti6Al4V alloy corrosion processes in aqueous solutions.

The higher values of ΔH_a in the inhibited (200 mg/L TCC) solution are caused by the strong corrosion-inhibiting activity. Furthermore, Figure 7 illustrates the correlation between log Icorr/T versus T⁻¹/K⁻¹, which is used to determine the values of ΔH_a and ΔS_a. The fact that the value of ΔH_a for TCC is more than that in the absence of TCC indicates that the corrosion rate of the Ti6Al4V alloy in an SS has decreased [65]. The activation entropy ΔS_a is negative and high with and without TCC (Table 4). Disorder decreases as one moves from reactants to activated complexes. This suggests the activated complex in the rate-determining step is an association step, not a dissociation step [65]. The low positive value of ΔH_a and the decline in inhibitory efficiency with temperature in the current investigation serve as evidence of physisorption. The apparent activation energy of the corrosion is higher in the presence of TCC (35.79 kJ mol⁻¹) than in its absence (14.46 kJ mol⁻¹).

3.2.2. Impedance Analysis

At different temperatures (310, 320, 330, and 340 K), EIS measurements are carried out in an SS both with and without TCC. Figure 8a,b uses the Nyquist plots to illustrate a single capacitive loop with a high polarization resistance. The Nyquist figure illustrates how the semicircle diameter decreases when TCC desorbs from the Ti6Al4V surface at high temperatures. As seen in

Table 5. Fitting parameters of EIS obtained for a Ti6Al4V alloy in an SS with and without TCC at different temperatures.

Temperature K	Rs (Ω cm2)	Rct (kΩ cm2)	CPEdl (F cm2 HZ1−n1)	n	$\mathsf{\Theta }$	ղEIS (%)
0.00 mg/L
310	16.79	7.80	79.61 × 10−6	0.843	-	-
320	22.36	6.12	123.80 × 10−6	0.829	-	-
330	44.19	5.43	235.11 × 10−6	0.788	-	-
340	76.15	4.49	310.74 × 10−6	0.769	-	-
200 mg/L
310	55.53	78.79	22.64 × 10−6	0.855	0.901	90.10
320	23.14	32.15	57.20 × 10−6	0.812	0.809	80.90
330	75.04	15.90	75.42 × 10−6	0.755	0.658	65.80
340	14.06	7.57	94.12 × 10−6	0.787	0.406	40.60

, adding TCC to an SS at any given temperature raises the R_ct value compared to the solution without TCC at that temperature. The decrease in R_ct values of TCC with rising temperature indicates that the desorption of TCC from the Ti6Al4V surface leads to lower surface coverage of TCC on Ti6Al4V, higher corrosion rate, and subsequently decreased inhibitory efficiency.

3.3. Adsorption Isotherm

The adsorption of TCC molecules at the Ti6Al4V/SS interface is explained by the following equation, which shows how organic molecules (TCC) replace water molecules:

TCC_sol + nH₂O_ads ↔ TCC_ads + nH₂O_sol

(8)

where n represents the number of water molecules that have been replaced, and TCC_sol and TCC_ads are the TCC compounds in the solution (liquid phase) and adsorbed on TCC-Ti6Al4V (adsorption phase), respectively [66]. The main factor influencing an organic compound’s capacity to reduce corrosion is its capacity to adsorb onto the TCC-Ti6Al4V surface.

Knowledge of the mode of adsorption was necessary to comprehend the way of interaction between the TCC molecules and the surface of the alloy. Several adsorption isotherms were employed to analyze the investigated TCC’s adsorption behavior. The Langmuir adsorption isotherm greatly matched the adsorption behavior of TCC at the Ti6Al4V/solution interface. Plotting C_inh/θ against C_inh using data generated from both polarization and EIS approaches yields straight lines with R² values of 0.9924 (Figure 9). Based on the Langmuir adsorption isotherm, which is described as follows [67]:

C_inh/θ = 1/K_ads + C_inh

(9)

where C_inh is the TCC concentration, K_ads is the adsorption equilibrium constant, and θ is the amount of surface coverage (θ = (ղ (%)/100). Conversely, the standard adsorption-free energy, or ΔG^o_ads at 310 K, was estimated using the following formula [67]:

ΔG^o_ads = −RT ln (55.5 K_ads)

(10)

where 55.5 is the molar concentration of water, R is the universal gas constant, and T is the Kelvin temperature. Physisorption is known to work well with ΔG^o_ads that have values of −20 kJ mol⁻¹ or lower, but chemisorption is necessary for those that have values greater than −40 kJ mol⁻¹ [68]. The ΔG^o_ads value was used to represent the adsorption type. Using the polarization and impedance results, the TCC’s calculated ΔG^o_ads value is −49.02 kJ mol⁻¹ and −49.20kJ mol⁻¹, respectively. A negative ΔG^o_ads value points to TCC adsorption on the Ti6Al4V surface occurring spontaneously (

Table 6. The equilibrium constant of the inhibitor (K_ads), the standard free energy of adsorption (ΔG^o_ads) for Ti6Al4V alloys in an SS containing 200 mg/L TCC concentrations at 310 K, was deduced by utilizing the Langmuir adsorption isotherm from the polarization and impedance data.

Alloy	Kads (L mol−1)		ΔGoads (kJ mol−1)
	Polarization	Impedance	Polarization	Impedance
Ti6Al4V	10.87 × 104	11.50 × 104	−49.02	−49.20

), suggesting that physisorption is the primary mechanism of TCC adsorption on the Ti6Al4V surface, and the possibility of partial chemisorption cannot be excluded. Based on polarization and impedance measurements, the equilibrium constant’s (K_ads) value may be calculated and found to be 10.87 × 10⁴ and 11.50 × 10⁴, respectively. The capacity of the adsorption forces among the TCC molecule and the alloy surface can be ascertained using the K_ads value. The greater K_ads value demonstrated the inhibitor’s superior adsorption capacity onto the Ti6Al4V surface.

3.4. Surface Morphology

To verify the mechanism of Ti6Al4V alloy degradation after corrosion in an SS, the electrode was investigated under a scanning electron microscope. Figure 10 displays the morphology of the surface of a polished Ti6Al4V alloy sample (Figure 10a) and the Ti6Al4V samples following a 24 h immersion in SS with and without a TCC inhibitor (Figure 10b,c). The barrier effect of alloy corrosion products in a given environment is determined by the characteristics and features of the resultant layer. The properties of thickness, homogeneity, compactness, porosity, solubility, fragility, and adhesion will influence the attack morphology and the corrosion rate of the underlying metal. As displayed in Figure 10b, the Ti alloy submerged in SS experiences surface degradation in the SS. However, the micrographs demonstrate that when TCC is present, it forms a superior protective film that covers the entire alloy surface and protects it from deterioration (Figure 10c). This indicates that the inhibitory efficiency of the TCC is superior. The EDS measurements on the polished surface (Figure 10d) and for the alloy surface with and without inhibitor molecules (Figure 10e,f) show that the sample immersed in TCC contains N elements. This is an additional indication that the shielding layer is created by the TCC’s adsorption on the alloy surface.

The UV spectra of TCC were measured both before and after the corrosion investigation to confirm the TCC inhibitor adsorption on the Ti alloy surface (Figure 11). The corrosive media in which the Ti6Al4V sample was not immersed had a higher absorbance, as indicated by the UV spectra, than the setting where the sample was dipped for a whole day. When the Ti6Al4V sample was immersed, some of the molecules from the TCC solution were adsorbed onto the surface. This implies that TCC has significant corrosion inhibition efficiency because it adsorbs on the Ti alloy sample effectively.

3.5. Contact Angle (CA) Approach

Contact angle evaluations were made to confirm that a shielding cover of the TCC layer had formed on the Ti6Al4V alloy. A 4.0 μL drop of water was applied to the alloy surface to take this measurement. The images showing the CA evaluations for the Ti alloy polished substrate (Figure 12a) and for the submerged Ti alloy in SS without (Figure 12b) and with TCC inhibitor (Figure 12c) are explored. When the polished alloy sample (Figure 12a) was dipped in the SS, its CA dropped from 68.8 ° to 32.8 ° (Figure 12b). This decrease suggests that the SS’s corrosive activity has increased the surface’s wettability. On the other hand, the contact angle of the alloy dipped in the TCC rose to 90.3° (Figure 12c). The adsorption of TCC on the Ti6Al4V alloy surface is shown by this notable increase in the CA, which suggests a decline in wettability and a rise in hydrophobicity. The formation of a hydrophobic shielding layer on the Ti alloy substrate successfully reduces the surface’s interface with water, as confirmed by the increase in CA upon the introduction of the TCC. By acting as a safeguard and preventing the damaging environment from destroying the SS superficial. This protective coating confirms that the TCC inhibitor is effective in preventing degradation.

3.6. Atomic Force Microscopy (AFM)

AFM is widely used to examine metal external morphology at the micro- and nano-scale levels in research examining the efficacy of corrosion inhibitors. The average surface roughness (Ra) evaluations of the Ti6Al4V alloy for the inhibited and uninhibited circumstances are carried out before and after a 24 h immersion in SS. For comparison, the Ra for the polished sample is explored as shown in Figure 13a. The data unequivocally demonstrate that adding the TCC inhibitor causes a considerable drop in the Ra values for Ti6Al4V alloy in aqueous SS, and that this drop increases with increasing TCC dosages. By extending coverage on the alloy’s surface and reducing the solution’s corrosive effect, the TCC particles create protective layers, which is the cause of the observed phenomena. The three-dimensional AFM images of a very glossy Ti6Al4V alloy surface with a Ra value of 116 nm are explained in Figure 13a. The Ti6Al4V alloy surface is shown in Figure 13b,c before and after a 24 h immersion at 37 °C in an aqueous SS, with Ra values of 289 nm and 347 nm, respectively, with and without TCC molecules. When contrasted to the exterior morphology in aqueous SS without the TCC, these images demonstrate that the exterior morphology of the Ti6Al4V alloy, as measured by height sensors, stays remarkably smooth even when TCC is present. Its capacity to protect the Ti6Al4V alloy surface from erosion in the damaging SS environment is demonstrated by this smoothness, which shows how well TCC inhibits. The outcomes, which show a notable reduction in surface roughness and enhanced surface protection, validate the inhibitor efficacy of TCC.

3.7. DFT Approach

The recital of TCC as a corrosion inhibitor for Ti6Al4V alloy in artificial seawater (ASS) is further elucidated in

Table 7. Computed quantum chemical descriptors for the studied neutral TCC and protonated TCCH⁺ inhibitor in the gas phase.

Descriptors	Equations	TCC	TCC H+
Energy of highest occupied molecular orbital (EHOMO), (eV)		−4.291	−3.981
Energy of lowest unoccupied molecular orbital (ELUMO), (eV)		−2.112	−3.601
Energy Gap ΔE	(LUMO-HOMO)	2.179	0.380
Dipole moment, (µ), (Debye)		1.983	19.758
Ionization energy (I) (ev)	$I={-E}_{HOMO}$	4.291	3.981
Electron affinity ($Y$) (ev)	$Y={-E}_{LUMO}$	2.112	3.601
Electronegativity (ϕ)	ϕ = ${\displaystyle \frac{I+Y}{2}}$	3.201	3.791
Global hardness ψ	ψ = ${\displaystyle \frac{I-Y}{2}}$	1.089	0.190
Global softness (S)	s = ${\displaystyle \frac{1}{\psi }}$	0.918	5.263
Global electrophilicity (ω)	ω = ϕ2/2ψ	4.705	37.820
Global nucleophilicity (ε)	$\mathsf{\epsilon }={\displaystyle \frac{1}{\mathsf{\omega }}}$	0.212	0.026
Electroaccepting (ω+) power	${\omega }^{+}={\displaystyle \frac{{\left(I+3A\right)}^2}{16\left(I-A\right)}}$	3.239	35.948
Electrodonating (ω−) power	${\omega }^{-}={\displaystyle \frac{{\left(A+3I\right)}^2}{16\left(I-A\right)}}$	6.441	39.739
Net electrophilicity (Δω± = ω+ +ω−)	(Δω± = ω+ + ω−)	9.680	75.687
Fraction of transferred electrons (ΔN)	$∆N={\displaystyle \frac{{\varphi }_{\mathrm{T}\mathrm{i}-}{\varphi }_{\mathrm{i}\mathrm{n}\mathrm{h}}}{2({\psi }_{\mathrm{T}\mathrm{i}}+{\psi }_{\mathrm{i}\mathrm{n}\mathrm{h}})}}$	−0.087	−0.108
Back-donation energy ΔE back-donation (ev)	${\mathsf{\Delta }\mathrm{E}}_{\mathrm{b}\mathrm{a}\mathrm{c}\mathrm{k}-\mathrm{d}\mathrm{o}\mathrm{n}\mathrm{a}\mathrm{t}\mathrm{i}\mathrm{o}\mathrm{n}}=-{\displaystyle \frac{\psi }{4}}$	−0.272	−0.047
Metal/inhibitor interaction energy ΔETi6Al4V/inhibitor (ev)	${\mathsf{\Delta }\mathsf{{\rm E}}}_{steel/Ti6Al4V}={\displaystyle \frac{{({\chi }_{Ti}-{\chi }_{inh)}}^2}{4({\eta }_{Ti}+{\eta }_{inh})}}$	0.593	216.352

, which summarizes the computed quantum chemical descriptors. Figure 14 and Figure 15 show the customized molecular structure of TCC, as well as its Frontier Molecular Orbitals (HOMO and LUMO). The HOMO orbitals were primarily concentrated on the ring structures and heteroatoms of the TCC molecule, indicating that these regions are good targets for electrophilic attack at the metal interface. This electronic configuration enhances the molecule’s inhibition efficiency, supporting the hypothesis that TCC can adsorb effectively onto the alloy surface, in alignment with the experimental findings. Furthermore, the energy gap (ΔE = E_LUMO − E_HOMO) plays a critical role in this adsorption process and is considered a key factor affecting the inhibitory performance of the molecule’s [41,48].

Table 7 presents the electrophilicity index (ω) and nucleophilicity index (ε) for both the neutral and protonated forms of the TCC inhibitor. In this study, the relatively low ω value indicates that TCC functions effectively as a nucleophilic corrosion inhibitor. The electron-accepting and electron-donating capabilities of the inhibitor are described by the electron-accepting power (ω⁺) and electron-donating power (ω⁻), respectively. A low ω⁺ value suggests a strong electron-donating ability, while a higher ω⁺ value implies enhanced charge-accepting capacity.

The interaction between TCC and the electrode surface is further characterized by the back-donation energy (ΔE), which reflects the stabilization gained from charge transfer during the adsorption. A negative ΔE value supports the occurrence of back-donation, contributing to increased inhibition efficiency. Specifically, Table 7 reports ΔE values of −0.272 eV for neutral TCC and −0.047 eV for its protonated form, TCCH⁺. Additionally, the fraction of electrons transferred (ΔN) between the inhibitor and the alloy surface is presented in Table 7. The data display that when ΔN is lower than 3.6, the inhibitors can donate electrons to the Ti alloy, which enhances their protective behavior. The interaction energy (ΔE) between the Ti6Al4V alloy surface and the TCC is a critical factor in evaluating the inhibitor’s effectiveness. As shown in Table 7, the interaction energy for the neutral TCC molecule is 0.593 eV, while for the protonated form, it significantly increases to 216.352 eV, indicating a stronger adsorption tendency and, consequently, improved corrosion inhibition performance. The electron-donating capacity of the tested inhibitor was evaluated based on the fraction of electrons transferred (ΔN) to the metal surface. Additionally, the local reactivity of the TCC molecule was assessed using Fukui function calculations, providing further insight into its reactive sites and interaction potential with the alloy surface TCC [43,44].

The best sites for nucleophilic and electrophilic strikes in TCC molecules were determined by Fukui indices. The electrophilic attack is preferred when f⁻_k has the maximum value and Δf_k < 0, while the f⁺_k value is maximum and Δf_k > 0, the area in the molecule is liable to nucleophilic attack [42,46]. The Fukui indices for both the neutral and protonated forms of TCC and TCCH⁺ are recorded in

Table 8. Fukui indices of the studied TCC.

Atom	f(+)	f(−)	∆fk	Mulliken Atomic Charges
C(1)	0.008	0.010	0.002	−0.091
N(2)	0.046	0.040	0.006	−0.115
C(3)	−0.019	−0.021	0.002	0.013
S(4)	0.101	0.360	0.259	−0.144
C(5)	−0.020	−0.022	0.002	−0.091
C(6)	0.111	−0.004	0.107	−0.022
N(7)	0.129	0.032	0.097	0.275
O(8)	0.047	−0.004	0.043	−0.035
C(9)	−0.036	−0.012	0.024	−0.338
C(10)	0.042	0.000	0.042	0.469
O(11)	0.081	0.001	0.080	−0.355
N(12)	0.021	0.005	0.016	0.404
N(13)	0.009	0.003	0.006	−0.136
C(14)	−0.002	−0.004	0.002	−0.479
S(15)	−0.008	0.023	0.015	−0.373
C(16)	−0.001	−0.006	0.005	0.042
C(17)	0.008	0.020	0.012	−0.203
C(18)	−0.001	−0.004	0.003	−0.192
C(19)	0.005	0.002	0.003	−0.075
O(20)	0.022	0.008	0.014	−0.192
C(21)	−0.018	−0.005	0.013	0.309
H(22)	0.024	0.017	0.007	−0.39
C(23)	−0.004	0.009	0.005	0.308
O(24)	0.011	0.047	0.036	−0.448
O(25)	0.009	0.043	0.034	−0.448
C(26)	0.002	0.000	0.002	−0.192
O(27)	0.001	0.002	0.001	−0.075
C(28)	0.005	0.000	0.005	−0.192
O(29)	0.009	0.002	0.007	0.309
N(30)	0.013	0.060	0.047	−0.39

. Notably, the inhibitor contains high-value sites that preferentially transfer electrons to the alloy’s unoccupied orbitals.

The highest f⁺_k and Δf_k values are S4, C6, N7, O8, C10, and O11 atoms in TCC, indicating that ideal sites for nucleophilic attack. In contrast, the most negative value of Δf_k and the largest value of f⁻_k at N2, S15, O24, O25, and N30 in TCC show that these sites are more frequently attacked by electrophiles. Additional active sites are developed upon protonation, resulting in a significant alteration of the active sites present in the neutral molecule. For protonated molecules, the preferred sites for nucleophilic attack are S4, C6, and O8 in TCCH⁺, presented in Table 8. Finally, the negative atomic charge values after protonation are slightly reduced from the TCC inhibitor’s potential interaction sites on the surface [69].

The electrostatic potential (ESP) and molecular electrostatic potential (MEP) maps of the neutral TCC molecule are shown in Figure 16. The electron density is orderly in the following order: red > orange > yellow > green > blue [70,71]. The potential surrounding the rings is positive in our study. In contrast, the potentials are negative, which are around heteroatoms such as nitrogen, sulfur, and oxygen, implying the essential site for electrophilic attack.

3.7.1. Natural Bond Orbital (NBO) Analysis

Natural Bond Orbital (NBO) analysis provides insights into charge transfer within a molecule and its influence on molecular stability, particularly through the evaluation of atomic interactions. The second-order interaction energy (E²) helps identify electron delocalization from filled orbitals—either bonding (BD) or lone pairs (LP)—to empty anti-bonding orbitals (BD*), thereby contributing to molecular stabilization, NBO [72]. In NBO terminology, BD refers to bonding orbitals formed between atoms, LP indicates lone pairs localized on individual atoms, and RY (Rydberg) represents orbitals with the highest principal quantum number and energy level, typically weakly bound or diffuse [73]. Second-order perturbation energy results derived from NBO analysis are widely utilized to assess hybridization, non-covalent interactions, and the overall stabilization of molecular systems. These results offer valuable insights into contributions from hyperconjugation, resonance, and other electron delocalization effects that impact the molecule’s electronic structure and reactivity [74,75].

Table 9. Second-order perturbation theory analysis of Fock Matrix in NBO Basis of TCC compound at B3LYP/6-311++G (d,p) level in the gas phase.

Compound	Donor	Acceptor	E(2) a (kcal/mol)	Occupancy
TCC	πC12–O41	π*C13–O40	22.52	1.67
	πC19–O15	π*C11–C13	21.13	1.65
	LP (1) N37	π*S54–N37	13.19	1.87
	LP (1) O23	π*O14–C6	50.05	1.74
	LP (1) O24	π*O23–O15	16.74	1.75
	LP (1) O25	π*C13–O26	45.21	1.88
	LP (1) O26	π*C32–O15	36.58	1.69
	LP (1) O27	π*C10–O24	26.47	1.57
	LP (3) S54	π*O14–N37	31.04	1.35
	LP (2) O14	π*S54–H57	29.83	1.82
	LP (2) O15	π*C10–C7	18.81	1.94
	LP (2) O16	π*C13–C11	28.83	1.82
	LP (2) O53	π*C13–O16	19.81	1.94
	LP (2) O41	π*C10–O15	33.04	1.37

^a Stabilization energy.

presents the 2nd-order perturbative energy results for the TCC compound, as determined in this study. The most significant stabilization energy contributions arise from the following electron delocalization interactions: LP(1) O23 → πO14–C6 (50.05 kcal mol⁻¹), LP(1) O25 → πC13–O26 (45.21 kcal mol⁻¹), and LP(1) O26 → πC32–O15 (36.58 kcal mol⁻¹). These interactions represent major resonance effects that enhance the stability of the TCC molecule. Additionally, electron delocalization from the lone pair on N37 to the antibonding orbital πS54–N37 contributes 13.19 kcal mol⁻¹ to stabilization energy. In summary, the TCC compound exhibits the highest second-order perturbation energy (E²), indicating a substantial contribution to electronic stabilization and, consequently, an enhanced corrosion inhibition efficiency compared to other inhibitors.

3.7.2. Molecular Simulation Dynamics

The adsorption behavior of the TCC inhibitor on the 101 ASS surface was investigated using molecular dynamics (MD) simulations. In the absence of solvent molecules, the interaction between the TCC molecule and the surface of Ti alloy (101) was examined within an isolated interactive system. The interaction energy (E__interaction) and binding energy (E__binding) of the created system were estimated using the following equations [76].

E_interaction = E_total − (E_{surface+ solution} − E_inhibitor)

(11)

E_bindi = −E_interaction

(12)

where E_inhibitor denotes the energy of an inhibitor molecule, and E_total denotes the total energy of the entire system under study, E_{surface+solution} denotes the total energy of the Ti (101) surface and solution without TCC inhibitor.

Figure 17 illustrates the use of the Layer Builder to position the TCC on the surface of Ti (101). For TCC, the calculated interaction energy was −763.27 kcal·mol⁻¹, while the binding energy was found to be 763.27 kcal mol⁻¹. As presented in Figure 18, the TCC inhibitor adsorbs in a parallel orientation to the Ti (101) alloy surface, achieving maximum surface coverage through interactions involving the π-electrons of aromatic rings, as well as oxygen, nitrogen, and sulfur atoms. These interactions result in strong adsorption, thereby enhancing the inhibition efficiency [77].

The chemical bonding between the TCC molecule and the Ti6Al4V surface of the 101 ASS was inspected using the radial distribution function (RDF) method [78,79,80]. Chemisorption is indicated by peaks appearing at distances of approximately 1 Å and 3.5 Å, while peaks beyond 3.5 Å correspond to physisorption [77]. As shown in Figure 19, the first obvious peak, seen at fewer than 3.5 Å, suggests the foundation of chemical bonds between TCC and Ti atoms. Moreover, the presence of peaks past 3.5 Å is attributed to physical interactions. The TCC inhibitor demonstrates a high capacity for donating and accepting electrons via active sites, which facilitates its adsorption onto the Ti6Al4V (101 ASS) surface and provides protection against dissolution. Our findings indicate that the TCC inhibitor exhibits mixed adsorption behavior, having both chemisorption and physisorption, as revealed by the RDF analysis. Furthermore, there is strong agreement between surface analysis, theoretical studies, molecular dynamics (MD) simulations, RDF results, and experimental measurements.

4. Conclusions

The first thorough examination of thiocolchicoside (TCC) as a corrosion inhibitor for Ti6Al4V alloy in a physiologically simulated 0.9% NaCl environment is presented in this work. Surface characterization and electrochemical methods showed that TCC offers superior corrosion protection, attaining an inhibition efficiency of up to 92.4% while preserving biocompatibility—a crucial characteristic for biomedical applications. According to the Langmuir adsorption isotherm, the physical adsorption of TCC molecules on the Ti6Al4V surface is principally responsible for the inhibition mechanism. The formation of a stable protective film was confirmed by the addition of 200 mg·L⁻¹ TCC, which increased the apparent activation energy from 14.46 to 35.79 kJ·mol⁻¹ and the polarization resistance from 7.85 to 78.88 kΩ·cm². The formation of a homogeneous inhibitor layer was confirmed by supporting analyses employing AFM, contact angle measurements, SEM, and UV-Vis spectroscopy. Strong adsorption energies, narrower energy gaps, and advantageous molecular orbital distributions that support strong metal–inhibitor interactions were also revealed by theoretical investigations (DFT, NBO, and MD simulations), which agreed with experimental findings.

Overall, this work presents TCC as a new and bioactive corrosion inhibitor for titanium alloys of biomedical grade and creates a theoretical and experimental framework for the development of more sophisticated inhibitors in the future. However, since theoretical modeling used an implicit solvent approach, more research that uses biological testing and explicit solvation is advised to more accurately represent actual physiological conditions.