Structure evolution during deposition and thermal annealing of amorphous carbon ultrathin films investigated by molecular dynamics simulations.

The evolution of the structure of amorphous carbon (a-C) films during deposition and thermal annealing is of significant interest from both the materials science and application perspectives. However, despite the voluminous literature of studies dealing with the deposition and physical properties of a-C films, basic understanding of the structure evolution due to phase change during film growth and heating is fairly sparse and empirical, presumably due to the lack of high-resolution instruments that can probe structural changes at the atomic and molecular levels in real time. Molecular dynamics (MD) is a powerful computational method for studying atomic/molecular-scale movement and interactions. Thus, the objective of this study was to perform MD simulations that provide insight into changes in the structure of ultrathin a-C films during deposition and annealing. Simulation results reveal a multi-layer film structure, even for a-C films as thin as ~20 Å, the existence of a deposition energy that yields a-C films with the highest sp3 content, the transient and steady-state stages of the structure evolution during annealing at different temperatures, and the changes in the hybridization state (mainly in the bulk layer) encountered during annealing at elevated temperatures. The MD results of this study are of particular importance to applications where the deposition conditions and operation temperature affect the structure and, in turn, the physical properties of ultrathin a-C films used as protective overcoats.


Analytical Methodology
Interatomic potential function. In all the MD analyses of multi-atom systems where interatomic forces are described by a potential energy function, atomic movement is determined by solving a set of differential equations of motion. Commonly used interatomic potential energy functions, such as the one-, two-, and three-body potentials, provide a description of the atom positions. However, these interatomic potentials may fail to describe the different bonding states of atoms, such as carbon and silicon. This inadequacy can be remedied by a bond-order potential that couples a two-body potential with a multi-atom correlation 27 . Using the so-called Tersoff potential, the total energy E of an atomic system can be expressed as where E i is the potential energy of atom i, V ij is the bonding energy between atoms i and j, r ij is the distance between atoms i and j, f C is a smooth cutoff function used to generate a gradual energy decrease to zero with increasing atomic distance, f R and f A are repulsive and attractive two-body potentials, respectively, and b ij is termed the bond order and represents the bond strength in the local environment, i.e., the bond strength of atoms having more neighboring atoms is characterized by a lower potential energy. The potential parameters are obtained by theoretical and experimental fits of the cohesive energy of element configurations. The first two elements to be fit with the Tersoff potential are carbon and silicon 27,28 . More details about the Tersoff potential can be found elsewhere 29,30 . Simulation procedure. As mentioned earlier, the MD simulations of the present study comprise two phases: (1) a-C film growth on a Si(100) substrate for various carbon atom kinetic energies and (2) thermal annealing at various temperatures. Film growth was simulated on a 23 × 23 × 59.7 Å silicon substrate consisting of 1620 atoms (Fig. 1). To model an infinitely large deposition area, periodic boundary conditions were applied to the lateral sides of the substrate. The silicon substrate atoms are classified in three categories, shown by different colors in Fig. 1. To simulate a semi-infinite substrate, the two lattice layers at the bottom of the MD model consisting of yellow atoms were fixed. The hollow prism made of red atoms is a Berendsen heat bath that controls the temperature during the simulation process 31 . The green atoms inside the hollow prism of red silicon atoms are free to interact with the incident carbon atoms. This model dissipates the internal energy rise caused by incident carbon atoms and maintains the substrate temperature at the desired level.
Before initiating carbon atom deposition, the silicon substrate was allowed to relax so that to minimize both the energy and the internal stress in the system. This was accomplished by increasing the temperature from 300 to 800 K, maintaining the temperature at 800 K for 5 ps, and finally cooling to 300 K. Thermal relaxation prevented the development of high internal stresses due to the effect of surface tension. After the relaxation of the silicon substrate, 2000 carbon atoms were randomly introduced one at a time from a height of 57 Å above the substrate surface and with velocity normal to the substrate surface. Using a time interval of 2 ps between sequential carbon atom injections allowed the system to relax and reach equilibrium via the Berendsen heat bath using a damping constant of 100 fs. Considering that the thermal spikes generated by bombarding energetic particles of kinetic energy less than 100 eV typically last for less than 0.5 ps 32 , using a time interval of 2 ps was adequate for simulating film growth for a particle kinetic energy of less than 120 eV. In all the deposition simulations, the time step was fixed at 0.5 fs and the heat bath temperature was set at 300 K.
In the thermal annealing simulations, the a-C film formed in the deposition phase of the simulation was kept at a constant temperate for 50 ns. The temperature was controlled by the Berendsen heat bath using a damping constant of 100 fs. In all the annealing simulations, the time step was fixed at 0.1 fs. All the MD simulations were performed with the Large-scale Atomic/Molecular Massively Parallel Simulator (LAMMPS) using a node with a 20-core Intel Xeon E5-2670 CPU. To validate the MD model, several simulations were performed to determine the time step and model dimensions that did not affect the results. Representative results from these simulations are shown in Fig. S1 of the Supplementary Information (SI). The yellow atoms at the bottom of the model are fixed to simulate a semi-infinite bulk substrate. The red atoms comprise a Berendsen heat bath that is used to control the temperature of the whole model. The green atoms that are fully surrounded by the thermostat atoms can freely interact with incoming carbon atoms.

Results and Discussion
Film growth. Figure 2 shows a-C film growth on a silicon substrate for a carbon atom kinetic energy in the range of 1-120 eV. Silicon and carbon atoms are shown in green and yellow colors, respectively. The bombardment of carbon atoms changes the crystalline structure of the silicon substrate, leading to the formation of an amorphous layer at the surface, hereafter referred to as the intermixing layer. The atoms in the intermixing layer comprise various silicon components bonded to neighboring silicon or carbon atoms. The intermixing layer acts as an adhesion layer that bonds the a-C film to the silicon substrate. The thicknesses of the intermixing layer and the a-C film strongly depend on the kinetic energy of the incident carbon atoms. The carbon atoms with a high kinetic energy can penetrate deeper into the substrate, producing a thicker intermixing layer. The intense bombardment of high energy (i.e., ≥80 eV) carbon atoms also causes a small fraction of silicon atoms to migrate into the a-C film.
The coordination number of carbon atoms affects the structure and properties of the a-C film significantly. This number is defined as the number of nearest neighbor atoms and is indicative of the hybridization state, i.e., a coordination number equal to 4, 3, and 2 implies sp 3 (tetrahedral, diamond-like), sp 2 (trigonal, graphite-like), and sp 1 (linear) hybridization, respectively. The coordination number of an atom depends on the cutoff distance of the nearest neighbor atoms. The position of the minimum between the first peak (r 1 ) and the second peak (r 2 ) of the radial distribution function is a plausible choice for the cutoff distance. Typical values of r 1 and r 2 for C-C bonds are 1.45 and 2.55 Å, whereas for C-Si bonds r 1 and r 2 are equal to 1.85 and 2.85 Å, respectively. In the present study, the cutoff distance for C-C bonds was set at 1.9 Å, while that for C-Si bonds was set at 2.0 Å, which is close to the 2.1 Å cutoff distance used in previous works 33,34 . Because carbon atoms can form bonds with both carbon and silicon atoms, the sp 2 and sp 3 contents reported here include both C-C and C-Si bonds. Although over-and under-coordinated carbon atoms may co-exist, they represent a very small fraction. Specifically, very few (0.7%) under-coordinated carbon atoms (coordination number = 1) were found at the film surface, which are attributed to the limited atomic bombardment of the outermost atomic plane and the effect of surface relaxation. A very small amount (3.9%) of over-coordinated carbon atoms (coordination number = 5) was found in the as-deposited film structure. Within a very short time from the inception of thermal annealing, all the over-coordinated atoms attained a more stable state corresponding to a coordination number of 2, 3, or 4. Consequently, the effect of under-and over-coordinated carbon atoms on the film structure was secondary. Figure 3(a) shows the sp 3 , sp 2 , and sp 1 hybridization contents and the relative density of the a-C film (defined as the ratio of the film density to that of diamond) versus the deposition energy of carbon atoms. Low deposition energy (e.g., 1 eV) yields a low density and mostly sp 2 -hybridized a-C film forming by carbon atom physisorption. A graphite-like film structure (~72% sp 2 ) is produced because the low kinetic energy of impinging carbon atoms is not effective in breaking the thermodynamically stable sp 2 and sp 1 carbon-carbon bonds. The increase of the carbon atom energy enhances carbon-silicon intermixing and sp 3 hybridization in the a-C film, resulting in a thicker intermixing layer (Fig. 2) and a thinner, denser, and more sp 3 -hybridized film structure ( Fig. 3(a)). Energetic incident carbon atoms can break existing carbon-carbon bonds (mainly the relatively weaker sp 1 and sp 2 bonds) and cause resputtering and/or recoil implantation, increasing the film density and promoting sp 3 hybridization. The highest sp 3 content (~48%) and relative density (~0.84) correspond to carbon atom deposition energy equal to 80 eV. Increasing further the deposition energy (e.g., 120 eV) decreases both the sp 3 fraction and the relative density of the film. This is attributed to localized relaxation prompted by thermal spikes and the greater prospect of sp 3 bond breakage and resputtering of deposited carbon material resulting from the intense atomic bombardment. All of the foregoing www.nature.com/scientificreports www.nature.com/scientificreports/ effects are conducive to graphitization. The similar variations of the sp 3 content and the relative density of the a-C film with the increase of deposition energy ( Fig. 3(a)) reveal a close dependence of film density on sp 3 content.
It is well-known that a-C films synthesized by energetic particle bombardment exhibit a multi-layer structure consisting of intermixing, bulk, and surface layers characterized by significantly different hybridizations 17,35,36 . The bulk layer possesses a much higher sp 3 content than the other two layers. The sp 3 content of the intermixing layer increases gradually from the substrate toward the interface with the bulk layer, while that of the surface layer decreases sharply from the interface with the bulk layer toward the film surface. To examine whether the MD model can simulate the multi-layer structure of a-C films, sp 3 depth profiles were computed by averaging the sp 3 content of 1-Å-thick slices through the film thickness. Figure 3(b) shows the effect of carbon deposition energy on the sp 3 depth profile of simulated a-C films. All cases reveal a sharply increasing sp 3 content at the film's interface with the silicon substrate (intermixing layer), a high sp 3 content in the middle region (bulk layer), and a sharply decreasing sp 3 content in the region adjacent to the film surface (surface layer). For very low deposition energy of 1 eV, the sp 3 depth profile is fairly flat, the sp 3 content is below 20%, and the intermixing layer is very thin, indicating the formation of a graphite-like a-C film that is slightly integrated with the substrate. Increasing the deposition energy to 80 eV not only enhances carbon-silicon intermixing, which is critical to the bond strength of the film to the substrate, but also decreases the film thickness and increases significantly the sp 3 content in the bulk layer, which controls the overall properties of the a-C film. However, the sp 3 content in the bulk layer decreases with the increase of the deposition energy to 120 eV, indicating the existence of an energy threshold for achieving the highest sp 3 content, in agreement with the experimental evidence 19 . Interestingly, all simulation cases show the formation of a surface layer with sp 3 content sharply decreasing toward the film surface, also in agreement www.nature.com/scientificreports www.nature.com/scientificreports/ with the results of a previous experimental study 15 . The formation of a graphite-like surface layer is attributed to less atomic bombardment than the bulk layer (because it forms at the end of the deposition) and surface relaxation resulting in a minimum energy state. During surface relaxation, the carbon atoms adjacent to the film surface migrate to lower energy sites where it is easier for them to become sp 2 hybridized and the decrease of the intrinsic compressive stress promotes sp 3 →sp 2 rehybridization.
The above simulation results and analysis suggest a film-growth process characterized by the sequential main phases depicted in Fig. 3(c-f). An animation of the film-growth process can be seen in Video A of the SI. During the initial deposition phase, carbon atom physisorption and/or implantation are the dominant physical mechanisms, depending on the kinetic energy of the carbon atoms, which control the formation of an ultrathin carbon layer on top of the intermixing layer. Newly arriving carbon atoms collide with previously deposited carbon atoms, knocking them deeper into the substrate (recoil implantation) and contributing to the formation of the intermixing layer ( Fig. 3(d)). An animation of recoil implantation where a carbon atom at the surface of the silicon substrate is knocked to a deeper location by an impinging energetic carbon atom can be seen in Video B of the SI. This deposition phase ends when the substrate becomes fully saturated with carbon atoms and carbon-silicon atom interaction diminishes. Next, the incident carbon atoms impinging onto the formed carbon atom planes lead to the growth of the bulk layer (Fig. 3(e)). The densification of the bulk layer and the evolution of high compressive stresses that are conducive to sp 3 hybridization and sp 2 →sp 3 rehybridization are encountered under deposition conditions of energetic atom bombardment (e.g., deposition energy of 80 eV). In the final deposition phase, the resputtering of weakly bonded carbon atoms decreases and the development of high compressive stresses for sp 3 hybridization diminishes due to less atomic bombardment of the topmost carbon planes. These effects together with surface relaxation are responsible for the formation of a surface layer rich in sp 2 hybridization (Fig. 3(f)). Table 1 shows the effect of the deposition energy of carbon atoms on the thickness of the intermixing, bulk, and surface layers. The boundaries of these layers were determined by computing the number of carbon atoms N c in each 1-Å-thick slice. The N c of the surface layer showed a sharp decrease, whereas that of the bulk layer remained fairly constant. The thickness of each layer was consequently determined from its known boundaries with other layers. For low deposition energy (e.g., ≤20 eV), penetration of the crystalline silicon structure by impinging carbon atoms is minimal; thus, the thickness of the intermixing layer is very small (2-3 Å). The increase of deposition energy (e.g., ≥80 eV) enhances carbon atom penetration, direct implantation, and recoil implantation in the silicon substrate, producing a significantly thicker intermixing layer. Indeed, for deposition energy equal to 80 and 120 eV, the thickness of the intermixing layer is 12 and 15 Å, respectively, corresponding to about 2.2 and 2.8 times the silicon lattice constant (5.431 Å). In contrast to the intermixing layer thickness, the bulk layer thickness decreases with increasing deposition energy because carbon atoms with a higher kinetic energy are implanted into the silicon substrate, contributing to the formation of a thicker intermixing layer than the growth of a thicker bulk layer. Nevertheless, the effect of carbon atom deposition energy on the surface layer thickness is secondary. This is attributed to less pronounced atomic bombardment of the surface layer in the last deposition phase and the effect of surface relaxation, as explained above. Thermal annealing. MD simulations of thermal annealing were performed for the a-C film with the highest (48%) sp 3 content, corresponding to carbon atom deposition energy of 80 eV (Fig. 3(b)). To examine the thermal stability of this film, simulations of thermal annealing were performed for a temperature between 150 and 450 °C. As stated earlier, the thermal stability of ultrathin a-C films is critical to the performance of devices operating at elevated temperatures, such as the HDDs designed for HAMR. Thus, the selected range of annealing temperatures is typical of the temperature range of a-C films used as protective overcoats of HAMR media. Figure 4 shows the overall sp 3 film content (computed as the average of the sp 3 contents of the intermixing, bulk, and surface layers) versus annealing time in the temperature range of 150-450 °C. The film's structural stability is determined by the minimum temperature that causes the sp 3 fraction to decrease sharply, resulting in sp 3 →sp 2 rehybridization. Annealing at 150 and 200 °C decreases the sp 3 fraction by only ~2%, whereas annealing at 250, 300, 350, and 450 °C decreases significantly the sp 3 fraction by 9%, 11%, 15%, and 17%, respectively. These predictions are in agreement with experimental results showing that annealing at 350 °C causes a decrease of the sp 3 content of a-C films deposited on various substrates by 4-16% 20 . For annealing at 300, 350, and 450 °C, the sp 3 content reaches a steady state in a very short time, indicating that rehybridization is a very rapid process. The increase of the annealing temperature decreases the time for the sp 3 fraction to reach a steady state. Table 2 shows the effect of annealing temperature on the thickness of the intermixing, bulk, and surface layers. The thickness of the surface layer increases with the temperature at the expense of the bulk layer thickness, while the thickness of the intermixing layer remains constant. The latter is in agreement with electron energy loss spectroscopy results  20 showing that annealing at 350 °C yields minor changes of the intermixing layer thickness of a-C films deposited on Au, SiN, NiCr, TaO x , and FeCo substrates.
Although Fig. 4 shows the evolution of the a-C film structure due to heating, i.e., sp 3 →sp 2 rehybridization, it does not provide insight into spatiotemporal changes of the film structure. Thus, to investigate localized changes in the film structure in the course of annealing, the variation of the sp 3 fraction through the film thickness with the annealing time and temperature was examined. As shown in Fig. 5(a,b), the effect of annealing at 150 and 200 °C on the spatial and temporal variation of the sp 3 fraction is practically insignificant, consistent with the invariance of the overall sp 3 content at these temperatures (Fig. 4). However, annealing at 250 °C causes a discernible decrease in the sp 3 content of the bulk layer (Fig. 5(c)), with the effect intensifying as the temperature is further increased (Fig. 5(d-f)). Different from the profound heating effect on the structure of the bulk layer, the effect of annealing on the structure of the intermixing and surface layers is much less pronounced, although a similar decreasing trend of the sp 3 content of these layers is also observed with increasing temperature. For instance, annealing at 250 °C causes the overall sp 3 content to decrease by 9%, with a 12% decrease in sp 3 content sustained by the bulk layer, while the change of the sp 3 content of the intermixing and surface layers is relatively insignificant. Annealing at a temperature above 250 °C intensified the rehybridization process in the bulk layer, which controls the overall sp 3 content of the a-C film. Specifically, annealing at 300, 350, and 450 °C resulted in the decrease of the overall sp 3 film content and the bulk layer sp 3 content by 11% and 17%, 15% and 20%, and 17% and 25%, respectively. As with the overall sp 3 content, the sp 3 content at each depth also reached a steady state within a very short annealing time.
Additional insight into the evolution of the film structure was obtained by examining the spatial distribution of carbon atoms in sp 1 , sp 2 , and sp 3 hybridizations. This was accomplished by slicing the a-C film with 48% overall sp 3 content (Table 1) into ten 4-Å-thick horizontal (x-y) slices, as shown in Fig. 6. The spatial distributions of carbon atoms with different hybridizations reveal a multi-layer film structure. The first slice (z = 18 Å), representing the surface layer of the a-C film, contains a few carbon atoms that are mostly sp 2 hybridized. Thus, it may be inferred that the surface layer of the a-C film possesses a graphite-like porous structure of relatively low density. The slices corresponding to the bulk layer (2 Å ≤ z ≤ 14 Å) contain roughly the same number of carbon atoms, which is significantly higher than that of the surface layer. These slices show a gradual increase in sp 3 hybridization with increasing depth in the range 6 Å ≤ z ≤ 14 Å, followed by a slight decrease in sp 3 hybridization at a depth z = 2 Å, which is adjacent to the interface of the bulk layer with the intermixing layer. The slices assigned to the intermixing layer (z < 0) show a sharp decrease in sp 3 hybridization and carbon atom density with increasing depth. The foregoing variation of the sp 3 content of the surface, bulk, and intermixing layers is consistent with the sp 3 depth profile corresponding to a carbon atom deposition energy equal to 80 eV (Fig. 3(b)) and in qualitative agreement with experimental findings 19 .  Table 2. Thickness of intermixing, bulk, and surface layers comprising the multi-layer structure of a-C film with 48% sp 3 overall content obtained after annealing versus annealing temperature.
The data shown in Fig. 6 provide a reference for the annealing simulations. Figure 7 shows the number of carbon atoms in different hybridizations at various depths through the film thickness before and after thermal annealing in the temperature range of 150-450 °C. Figures 7(a,b) show that annealing at 150 and 200 °C, respectively, does not change significantly the carbon atom density and the hybridization state. However, as evidenced from Fig. 7(c-f), annealing at a temperature above 200 °C changes significantly the number of carbon atoms in each slice and also triggers sp 3 →sp 2 rehybridization, more notably in the bulk layer (0 ≤ z ≤ 13 Å). For instance, while annealing at 250 °C increases the number of carbon atoms in the surface layer (13 Å ≤ z ≤ 18 Å) by 29 (46%) and decreases those in the bulk layer (0 Å ≤ z ≤ 13 Å) by 32 (2.3%), annealing at 450 °C causes the carbon atoms in the surface layer to sharply increase by 84 (140%) and those in the bulk layer to decrease by 78 (5.5%). Carbon atom rehybridization induced by annealing decreases the sp 3 content of the bulk layer by 9% at 250 °C and 16.7% at 450 °C. Compared to the bulk and surface layers, the intermixing layer exhibits insignificant changes in carbon atom number at all temperatures. The carbon atom changes in the surface layer and the intermixing layer indicate atom migration during annealing, which is attributed to stress relaxation of the bulk layer. The increase of carbon atoms and insignificant hybridization changes in the surface layer indicate the development of a thicker surface layer as a result of annealing at an elevated temperature (i.e., >250 °C). The decrease of the number of carbon atoms and the sp 3 content of the bulk layer due to annealing in the temperature range 250-450 °C  In addition to the distributions and hybridizations of carbon atoms in horizontal slices through the film thickness, carbon atom hybridization in 4-Å-thick vertical (y-z) slices was also examined to identify any changes in the as-deposited film structure due to annealing at planes perpendicular to the film surface. Figure 8 shows sp 1 , sp 2 , and sp 3 hybridized carbon and silicon atoms in vertical slices before and after annealing at 450 °C. The simulations reveal two important results. First, only changes in hybridization can be observed after thermal annealing, www.nature.com/scientificreports www.nature.com/scientificreports/ whereas differences in the number of carbon atoms in each vertical slice are insignificant. In the light of this result and the periodic boundary conditions, it may be inferred that the film possesses a fairly uniform structure. Second, a comparison of carbon atom hybridizations in each slice before and after annealing shows a uniform trend for sp 3 →sp 2 rehybridization throughout the film structure, especially in the bulk layer.
In some elevated-temperature applications, the decrease of the sp 3 content of the protective a-C film as a result of heating may enhance its chemical reactivity, especially in an oxidizing atmosphere. The evolution of the a-C structure in a hot, oxidizing atmosphere could be more complex than that simulated for inert thermal annealing conditions. Thermal annealing in an oxidizing atmosphere may accelerate oxidation and material loss at the film surface, with the thermally excited oxocarbon molecules entering the oxidizing gaseous environment. The reaction of an oxidizing gas with the film in conjunction with the development of mechanical traction due to surface contact may promote or even accelerate carbon oxidation at elevated temperatures, thus degrading the structural integrity of the a-C film and, in turn, its protective effectiveness. The detrimental effect of oxidizing gas diffusion on the film's structural stability may be more pronounced than that of sp 3 →sp 2 rehybridization propelled by thermal effects. An MD analysis of ultrathin a-C films rich in sp 3 hybridization exposed to an elevated temperature in an oxidizing atmosphere is the objective of a forthcoming publication.

conclusions
A comprehensive MD analysis of energetic carbon atom deposition on silicon was performed to elucidate the growth process of ultrathin a-C films and identify the structural changes induced by thermal annealing. The MD simulations confirmed the multi-layer structure of a-C films synthesized by energetic particle deposition methods. The study of the effect of carbon deposition energy on the film growth characteristics revealed a deposition energy threshold for synthesizing a-C films of maximum density and sp 3 hybridization. By increasing the deposition energy toward the deposition energy threshold, the intensifying carbon atom bombardment promoted direct and recoil implantation and the development of high compressive stresses, which are conducive to film/substrate intermixing, preferential resputtering of weakly bonded atoms, sp 3 hybridization, and sp 2 →sp 3 rehybridization. However, for deposition energy above the deposition energy threshold, the intense bombardment of the growing film promoted resputtering and, presumably, the development of thermal spikes, which reduced the film density and high compressive stresses, favoring sp 2 hybridization and sp 3 →sp 2 rehybridization.
The MD simulations of thermal annealing of the a-C film with the highest sp 3 content (48%) in this study demonstrated insignificant structural changes for temperatures up to 200 °C, with progressively intensifying carbon atom migration in the intermixing and surface layers and sp 3 →sp 2 rehybridization in the bulk layer with the increase of temperature from 250 to 450 °C. While annealing increased the thickness of the surface layer, it decreased the thickness of the intermixing layer and the density of the bulk layer. An important finding is that sp 3 →sp 2 rehybridization at an elevated temperature is a very rapid process. Annealing at a relatively high temperature (e.g., 450 °C) may also have a negative effect on the film's permeability because it may create potential oxidizing gas diffusion sites.
The results of this study provide new insight into the dependence of the growth and structure of a-C films on deposition process conditions and annealing at various temperatures. The knowledge derived from the present MD simulations has direct implications on the physical properties of ultrathin a-C films used as protective www.nature.com/scientificreports www.nature.com/scientificreports/ overcoats of devices operating at elevated temperatures. The good agreement of the simulation trends and results of this study with experimental findings of earlier investigations validate the present MD model and employed analytical methodology. This work provides impetus for using the present MD modeling approach to guide the selection of appropriate film deposition and annealing conditions and to perform parametric studies aimed at tuning the multi-layer structure of a-C films according to specific application requirements.