The orientation of hydrocarbon chains plays a key role in the applications of organic materials. And chain folding in the process of molecular orientation is also of great significance for the design of organic molecular thin films. The effect of chain length and simulation temperature on the isothermal orientation of n-alkanes on graphene surface is studied by molecular dynamics simulation in this paper. And the chain folding is also described. The n-alkanes can form perpendicular ordered structure, parallel ordered structure or perpendicular orientation at relative low temperature and parallel orientation at relative high temperature on graphene surface. The chain fold happens when long n-alkanes form perpendicular ordered structure on graphene surface. And the simulation results show the interactions of n-alkane−graphene and n-alkane−n-alkane affect chain fold.
Research Article
Molecular Dynamics Simulations on the Chain Fold During the Isothermal Orientation of n-Alkanes on Graphene
https://doi.org/10.21203/rs.3.rs-901033/v1
This work is licensed under a CC BY 4.0 License
Version 1
posted 27 Oct, 2021
You are reading this latest preprint version
graphene
n-alkane
orientation
chain fold
molecular dynamics simulation
In recent years, due to the wide application of organic molecular thin films in industry, a lot of studies have been done in this field [1–4]. The organic thin films are prepared by adsorbing of organic molecules on surface at different condition. They share some common properties. Thickness is very small, the specific surface area is very large and anisotropy exists in a thin film. The different oriented organic films have different properties, which lead to different functions. The hydrocarbon chain is a basic component of many organic materials. The orientation of them in organic materials affects the physical properties and applications of the materials. Therefore, it is very important to understand the arrangement and orientation of hydrocarbon chains on surface for the industrial application of organic molecular thin films.
The experimental and molecular simulation studies for the orientation of molecules on surface have been carried out recently [5–36]. Yamamoto et al. [5] studied the crystallization process of n-undecane on flat substrate with different attractiveness by molecular dynamics (MD) simulation. They found that the film is composed of thin lamellae, in which the alkanes chain is parallel or perpendicular to the substrate. The thickness of thin films affects the orientation of molecules [5–8]. The thicker films on the strong attractive substrate are dominated by parallel lamellae, while the thinner films on the weaker attractive substrate are dominated by perpendicular lamellar layers. Fu et al. [9] found that the molecular orientation is related to chain length, by studying the orientation of linear alkanes n-C36H74 and n-C60H122 on the NaCl (001) surface.
And many studies found that substrate temperature has a significant effect on the molecular orientation in the n-alkane thin film [10–17]. Nozaki et al. [14] used X-ray diffraction and scanning probe microscopy to analyze the molecular orientation of the n-alkane evaporated film prepared under different deposition conditions. They found a "coexisting film" composed of perpendicular orientation and parallel orientation at low substrate temperature and high evaporation rate. Kubono et al. [15–16] studied the molecular orientation of different linear long-chain compounds in the process of vapor deposition and found that high substrate temperatures and low deposition rates resulted in a perpendicular orientation to the substrate surface; low substrate temperatures and high deposition rates resulted in a parallel orientation or an amorphous structure. Fukao et al. [17] found that the parallel orientation state of the molecule will change into a perpendicular orientation state, when n-alkane evaporation film is annealed below the melting point, and the change of molecular orientation is irreversible.
In addition, the molecular orientation of alkane at different interfaces was studied by MD simulation [18–21]. The difference of the orientation mechanism between water-vacuum interface and water-oil interface has been studied [18–20]. Qiu et al. [22] studied the relationship between the interface orientations of alkane in liquid phase by MD simulation. They found that alkane tends to be perpendicular to the alkane-vacuum interface and parallel to the alkane-water interface in the liquid phase.
Chain fold is a basic feature of polymer crystallization [23, 24]. In the past few years, a lot of studies have been done on polymer fold [23–37]. Ungar et al. [25, 26] studied on the monodisperse polymers and showed more information about polymer crystallization, such as integer folding, non-integer folding, lamellar thickening and the nature of fold surface and end surface. Hobbs et al. [27] found that the crystals of C294H590 can be grown in different integer fold forms from the dilute solution. At an appropriate temperature, the crystal will become thicker from the form of one fold to another. Iwata et al. [28] obtained the fold structure at both low and high temperatures and observed the sliding movements of a chain during the crystallization. Fujiwara and Sato [29, 30] studied the chain fold process of single molecular chain with 500 methylene groups by MD simulation. Kavassalis [31] and Shakirov [32] et al. found that the folded lamellar crystal for polyethylene (PE) chains requires a minimum chain length to occur as the ground state folded structure, which is around 150 methylene groups. In addition, substrate [33] influences the fold of the chain in the layered structure. Gulde et al. [34] found that polymers adsorbed on graphene surface form two-dimensional folded microcrystals. And chain fold was observed in polymer single crystal by atomic force microscope (AFM) [35–37]. However, none of the works showed whether alkane chain fold will occur in the process of molecular orientation on surface. This is one of important aspects of the formation mechanism for molecular orientation on surface and is also of great significance for the design of organic molecular thin films. Therefore, this paper will also focus on the chain fold in the process of molecular orientation on surface.
The selection of substrates is crucial in the study of the orientation of organic molecules on surface. Graphene is an ideal substrate for the preparation of high performance conductive thin films [38–40]. The two-dimensional supramolecular assembly of organic molecules on graphene surface can affect the structure of organic molecules and improve the properties of organic thin film materials [41–45]. Therefore, we choose graphene/alkane system for studying the orientation of the hydrocarbon chain on surface.
In our previous studies, we studied the isothermal orientation of n-decane (C10) between two graphene sheets [46]. The simulation temperature is very important for C10 orientation between graphene sheets. And we also studied the orientation of n-alkanes of different lengths on graphene [47]. The chain length affects the orientation of the n-alkanes on graphene. In this paper, we will continue to study the perpendicular orientation and parallel orientation of n-alkane on graphene surface. First, the final conformations of n-alkane molecules on graphene surface at different temperatures will be described. Second, the orientation process of n-alkanes on graphene surface will be presented. Thirdly, the fold behavior of n-alkane chains on graphene surface will be discussed, and the formation process of the different types of chain fold conformations will be analyzed. Finally, the effect of alkane-alkane interaction and alkane-surface interaction on the orientation of molecules will be discussed.
Ten kinds of n-alkane chains tridecane (C13), tetradecane (C14), pentadecane (C15), hexadecane (C16), heptadecane (C17), octadecane (C18), nonadecane (C19), icosane (C20), pentacosane (C25) and triacontane (C30) are chosen in this study. We first build 115C13, 107C14, 100C15, 94C16, 88C17, 83C18, 79C19, 75C20, 60C25, 50C30 and a graphene sheet with lattice parameters x = 51.4 Å, y = 49.2 Å, z = 120 Å, α = β = γ = 90°. Then the n-alkane chains are randomly placed on the graphene surface, respectively. The ten systems all contain about 1500 alkane carbon atoms. They are denoted as 115C13/GRA, 107C14/GRA, 100C15/GRA, 94C16/GRA, 88C17/GRA, 83C18/GRA, 79C19/GRA, 75C20/GRA, 60C25/GRA, 50C30/GRA, respectively. The first number is the number of alkane chains and the second number is the number of carbon atoms in the chain. 50000 steps of energy optimization are carried out to relax configurations. The 10000ps NVT MD simulation is performed at a relative high temperature. The initial configurations are obtained with n-alkane chain adsorbed on the graphene surface. Periodic boundary conditions are used in these systems. The cell parameter z is large enough to ignore the interactions between the adsorbed n-alkane and the periodic images of graphene surface in the z direction. By this way, the three-dimensional periodicity is transformed into two-dimensional periodicity. The graphene surface is free during all the simulations.
The n-alkane molecules are described in all-atom model. The COMPASS force field [48–50] has been used to simulate the interactions between alkane/polyethylene and graphite/graphene/carbon nanotube successfully [51–53]. Thus we choose COMPASS force field to describe our systems. The energy of the system calculated from the COMPASS force field includes valence and nonbonding terms. The valence terms include stretching, bending, and torsion energies as well as the diagonal and off-diagonal cross-coupling terms. The nonbonding interaction is mainly controlled by van der Waals and electrostatic interactions between the n-alkane chains and the graphene. The cutoff distance for the nonbonding interaction is 12.5Å. The 10000ps NVT MD simulations are performed for the systems in the temperature range of 300K ~ 550K. The integral time step is 1fs. Nose-Hoover thermostat [54–56] is used to keep the temperature constant in the systems.
3.1. The Isothermal Orientation Processes of 79C19/GRA at 450K and 490K
We acquire a greater depth of understanding the ordered structure formation of n-alkane via MD simulations. Our simulations show that C19 molecules are perpendicular to the graphene surface at relative low temperature (T ≤ 480K) and parallel to the graphene surface at relative high temperature (T > 480K). This is similar to our previous work [46–47]. The chain fold also is found for long n-alkane chains in our simulations. Thus, we also show the two typical isothermal orientation processes for 79C19/GRA at 450K and 490K in Fig. 1(a) and (b), respectively.
At the beginning of the simulation, C19 molecules are adsorbed on graphene surface and form disordered structure. At 450K, some C19 molecules are adsorbed near the surface and are parallel to the surface, and others are still disordered at 200ps. Local orientation appears at about 1000ps. After that, more C19 molecules move into the ordered region slowly and the orientation region become larger gradually. Most of C19 molecules are perpendicular to the surface at 2000ps. The perpendicular order degree increases with the simulation proceeding. Chain fold occurs when the ordered structure forms. The chain fold leads to the height of the perpendicular ordered region decreasing gradually. This has not been found when study the orientation process of short n-alkanes on or between graphene sheet(s) [46, 47]. At the end of the simulation, most of the C19 molecules are perpendicular to the surface, and they are also parallel to each other. It can also be seen that the ends of some C19 molecules near the surface is curved in the perpendicular ordered region.
At 490K, some of C19 molecules are also adsorbed near the surface and others are still disordered before 1000ps. Local orientation appears at about 2500ps. Some of C19 molecules are curved and others are extended in the first layer near the graphene surface before 2500ps. After that, more C19 molecules enter the ordered region quickly. At 3000ps, most of C19 molecules are parallel to graphene surface and form a six-layer structure. As the simulation going, the order degree of the six-layer structure increases. The molecules arranging in the six-layer structure are extended and parallel to each other. The effect of graphene on the orientation of C19 molecules results in the orientation starting in the first layer near the graphene surface and then in the next layer. At the end of the simulation, almost all C19 molecules arrange in the six-layer structure.
In summary, the two kinds of orientation processes are considered as a three-step process (adsorption, orientation, and growth). And C19 molecules tend to be perpendicular to graphene surface at relative low temperature and form parallel multi-layer structure at relative high temperature. This is similar to the isothermal orientation of n-decane between two-layer graphene [46]. But the C19 molecules fold in the perpendicular ordered region on graphene surface at relative low temperature. Our simulations also indicate that when the chain length is long enough, chain fold only occurs in perpendicular orientation. We compare the final conformations of n-alkane on graphene surface at different temperatures, the effect of chain length on the orientation of n-alkane on graphene surface can be identified and the critical chain length of n-alkanes with perpendicular and parallel orientation on the graphene surface can also be obtained.
3.2. The Effect of Temperature on the Orientation of n-Alkane on Graphene
The n-alkane chains may be perpendicular orientation, parallel orientation or perpendicular orientation at relative low temperature and parallel orientation at relative high temperature on the graphene surface. Figure 2 displays the final conformations of C13, C19, C25 molecules on graphene surface with the three typical orientations at different temperatures.
For 115C13/GRA, C13 molecules arrange in a disordered state at 300K. Almost all C13 molecules are perpendicular to the surface at 400K, 450K and 490K. The perpendicular order degree increases with temperature increasing. At 490K, some C13 molecules are desorbed from the surface and appear below the surface due to periodic boundary conditions. At 500K, more C13 molecules are desorbed and a disordered structure forms on graphene surface. For 79C19/GRA, a disordered structure form on graphene surface at 300K. C19 molecules are perpendicular to the surface at 400K and 450K. And the height of the perpendicular ordered regions are smaller than the extended C19 molecule shown in Fig. 2(b). The length of extended C19 molecule is 22.59Å. Chain fold occurs when the perpendicular ordered structure of C19 molecules forms. At 490K, almost all C19 molecules are parallel to graphene surface and are parallel to each other. They form a parallel multi-layer structure. At 500K, C19 molecules form a disordered structure on graphene surface. For 60C25/GRA, C25 molecules are disordered at 300K, and a few molecules adsorbed near the surface are parallel to the surface. More C25 molecules are parallel to graphene surface at 400K. At 480K and 500K, parallel multi-layer structures form on graphene surface. Almost all C25 molecules arrange in the ordered structure and are parallel to each other. At 550K, C25 molecules also form a disordered structure on graphene surface.
The n-alkane can form disordered structure, perpendicular ordered structure, parallel multi-layer structure on graphene surface. The final conformations of ten kinds of n-alkane molecules on graphene surface at all the temperatures are shown in figure S1 of the Supporting Information. Ten kinds of n-alkane molecules relax slowly and form disordered structures on graphene surface at 300K. The 115C13, 107C14, 100C15 and 94C16 only form the perpendicular ordered structures on graphene surface. The 88C17, 83C18 and 79C19 are perpendicular to graphene surface at relative low temperature and form parallel multi-layer ordered structure at relative high temperature. The 75C20, 60C25 and 50C30 only form parallel multi-layer structure. When temperature is high enough, the n-alkane molecules form disordered structures on graphene surface. In addition, when n-alkane molecule is longer than C15, chain fold occurs with perpendicular ordered structure forming on the surface. Some n-alkane chains fold into two or more stems during the MD simulation. And n-alkane chains adopt extended conformations in parallel multi-layer ordered structure on the surface.
The chain length affects the orientation of n-alkanes on graphene surface. When the n-alkane molecule is shorter than that of C17, they arrange perpendicularly to the graphene surface. And when n-alkane molecule is longer than C19, they form parallel multi-layer ordered structure on graphene surface. C17, C18 and C19 molecules are perpendicular to graphene surface at relative low temperature and form parallel multi-layer structure at relative high temperature. Thus the longest n-alkane chain that can form perpendicular orientation is C16 molecule on graphene surface. The shortest n-alkane chain that forms parallel multi-layer ordered structure is C20 molecule. And when the chain length is longer than C15, chain fold only occurs in perpendicular orientation region.
Is the orientation of (C17-C19) reversible with temperature i.e., perpendicular orientation at lower temperature and parallel orientation at higher temperature when annealing procedures are performed on them? This is interesting and important in the devising and manufacturing this kind of assembling material. Therefore, annealing procedure is performed on 83C18/GRA at the cooling rate of 10K/2000ps with the same parameters as our isothermal MD simulations. As the orientation of the simulated n-alkanes is sensitive to the cooling rate, another two annealing procedures are simulated at the cooling rate of 10K/1000ps and 10K/500ps. Snapshots of the last conformation of 83C18/GRA for various temperatures during the three annealing procedures are shown in figure S2 of the Supporting Information. The C18 molecules are first disordered at high temperatures and parallel to the surface with temperature decreasing during the annealing procedure at the cooling rate of 10K/2000ps. The C18 molecules first form disordered structure at high temperatures and are perpendicular to the surface with temperature decreasing at the cooling rate of 10K/1000ps and 10K/500ps. The orientation of C18 molecules are irreversible with temperature. The temperature of parallel orientation appearing is higher than that of perpendicular orientation. The C18 molecules are favorite forming perpendicular orientation at fast cooling rate and parallel orientation at slow cooling rate. Only one orientation appears for C18 during the annealing procedure. The parallel and perpendicular orientation can both obtained by isothermal MD simulations at different temperatures. These are useful information for manufacturing this kind of assembling material.
3.3. The Orientation Parameter of n-Alkanes on Graphene
In order to describe the orientation structure of n-alkanes with different chain lengths at different temperatures quantitatively, we calculate the global orientation order parameter g-OPb and the z axis bond-orientation order parameter of the n-alkanes. The global orientation order parameter g-OPb can describe the conformation of all alkane molecules, which is defined as
where φ refers to the angle between two neighboring subbond vectors, the center of the two adjacent bonds are connected to form the subbond vector (see the schematic drawing in Fig. 3). When g-is 1.0, all of the alkane chains are extended. The z axis bond-orientation order parameter is used to describe the orientation of alkane molecules on graphene surface, which is defined as
where ϕ is the angle between the subbond vector and the z axis. When the subbond vector is completely parallel to the z axis, = 1.0; when the subbond vector is perpendicular to the z axis, = -0.5; when the subbond vector is random to the z axis, = 0.0.
Figure 4 and 5 show the global orientation order parameter g-OPb and the z axis bond-orientation order parameter for C13, C19 and C25 molecules on graphene at different temperatures, respectively. For 115C13/GRA, the is about − 0.05 at 300K, indicating that C13 molecules are laid randomly on graphene surface. The increases from 0.7 to 0.9 and the g-OPb fluctuates around 0.95 from 400K to 490K, indicating that more C13 molecules arrange in the perpendicular ordered structure and adopt extended conformation. The is near − 0.1 and the g-OPb is about 0.55 at 500 K, indicating that disorder structure forms on the surface at 500 K.
For 79C19/GRA, the increases from − 0.1 to 0.7 in the temperature range of 300K ~ 480K, meaning that more C19 molecules change from random to perpendicular orientation to the surface. The is -0.4 at 490K, indicating that the C19 molecules are parallel to the surface. The g-OPb fluctuates around 0.73 in the temperature range of 300K ~ 450K, showing that C19 molecules are folding in the ordered structure. The g-OPb increases to 0.88 at 490K. This illustrates that most of C19 molecules adopt extended conformation at 490K. The is 0.0 and the g-OPb is 0.58 at 500 K, indicating that disordered structure forms on the surface at 500 K.
For 60C25/GRA, the g-OPb increases from 0.72 to 0.89 in the temperature range of 300K ~ 500K, which indicates that most of C25 molecules adopt extended conformation, and a small number of molecules are curved. The decreases to -0.4 from 300K to 450K and fluctuates around − 0.4 in the temperature range of 450K ~ 500K, indicating that C25 molecules are parallel to the surface. And the is -0.1 and the g-OPb is 0.55 at 550K as a result of a disordered structure forms on the surface.
Simulation temperature and chain length are important in the orientation of n-alkanes on graphene surface. Figure S3 and S4 show the global orientation order parameter g-OPb and the z axis bond-orientation order parameter for the ten kinds of n-alkane molecules on graphene at different temperatures, respectively. Ten kinds of n-alkane molecules are all randomly on graphene surface at 300K. When the chains are shorter than C17, molecules are perpendicular to the surface. For long chains (> C19), molecules are parallel to the surface. The C17, C18 and C19 molecules are perpendicular to surface at relative low temperature and form parallel multi-layer structure at relative high temperature on surface. When the temperature is high enough, ten kinds of n-alkane molecules all form disordered structure on surface.
3.4. Fold Behavior of n-Alkane Chains on Graphene Surface
In the previous sections, the orientation structure of n-alkane on graphene surface has been discussed. The chain fold happens when long n-alkane form perpendicular ordered structure on graphene surface. This section will explore the chain fold in details. First, we calculate the average end-to-end distance (Red) of n-alkane at different temperatures. It refers to the line distance from one end of the molecule to the other. When the molecular is extended, Red is equal to the length of extended molecule (Rall−trans). When the molecule curved or chain folding occurs, Red is smaller than the Rall−trans.
The average end-to-end distance of the last 1000 configurations of the ten kinds of n-alkane molecules at different temperatures are calculated and provided in figure S5 of the Supporting Information. The average Red of the ten kinds of n-alkane molecules are much less than their Rall−trans at 300K, meaning that molecules are curved at 300K. The average Red of 115C13, 107C14, 100C15, 75C20, 60C25 and 50C30 are close to their Rall−trans with the simulation temperature increasing, meaning that more molecules adopt extended conformation. But the 115C13, 107C14 and 100C15 are extended in the perpendicular ordered structure and the 75C20, 60C25 and 50C30 are extended in the parallel ordered structure on graphene surface. For 94C16/GRA, 88C17/GRA, 83C18/GRA and 79C19/GRA, the average Red at relative low temperature are less than the average Red of disordered structures, meaning that more molecules adopt curved conformation. Chain fold happens during the chains perpendicular orientation on the surface. The average Red is close to the Rall−trans when the four kinds of n-alkane molecules parallel orientation at relative high temperature on graphene surface. This means that most molecules are extended and chain fold does not occur in the parallel ordered structure. The average Red of the ten kinds of n-alkane molecules is less than their Rall−trans and close to the average Red of disordered structures when temperature is high enough, meaning that molecules are curved and disordered on graphene surface. In brief, the occurrence of chain fold is related to the chain length. And chain fold happens when the chains are longer than C15 and form perpendicular ordered structure on graphene surface. This also shows the three kinds of orientations for n-alkanes on graphene surface. The ratio of average Red to Rall−trans (Red/Rall−trans) of three typical systems (115C13/GRA, 79C19/GRA and 60C25/GRA) are shown in Fig. 6 as an example.
The time evolution of the average end-to-end distances during the two orientation process can help us to understand the chain fold process in detail. In order to check the chain fold behavior of 79C19/GRA with perpendicular ordered structure at 450K and parallel multi-layer structure 490K, Fig. 7 shows the time evolution of the average end-to-end distances of 79C19/GRA on graphene surface at 450K and 490K.
At 450K, the average Red of 79C19 increases to 17.0Å before 600ps, decreases to 10.3Å from 600ps to 8000ps gradually, and fluctuates around 10.3Å after 8000ps, which are smaller than their Rall−trans (22.59Å). The ratio of average Red to the film thickness of 79C19 is about 0.72. This means that the formation of perpendicular orientation is accompanied by chain fold. The height of the perpendicular ordered regions are smaller than the extended C19 molecule. It may be speculated that the height of the perpendicular ordered regions decreases owing to the chain fold during the simulation proceeding. At 490K, the average Red of 79C19 fluctuates around 15.8Å before 2000ps, increases to 20.0Å from 2000ps to 5000ps, and fluctuates around 20.0Å after 5000ps, which are close to their Rall−trans. This shows that most of C19 molecules change from curved conformation to extended conformation gradually during the orientation process. The C19 molecules do not fold in the parallel ordered structure.
The C-C-C-C torsion angle of C19 molecules are also calculated to describe the conformation at 450K and 490K. Figure 8 gives the torsion angle distributions calculated from the last 1000ps of the simulations. There are two kinds of peaks in the distribution. The first one is the torsion angle between 30° ~ 100° or -30° ~ -100°. The peak indicates the presence of the gauche conformation. The second one is the torsion angle between 150° ~ 180° or -150° ~ -180°. The peak means that the presence of the trans conformation. The second peak is much higher than the first one. This means most of C19 molecules adopt trans conformation. For the peak between 30° ~ 100°or -30° ~ -100°, the height at 450K is higher than that at 490K. This indicates that more C19 molecules are gauche conformation at 450K. This results from the occurrence of chain fold in the perpendicular ordered structure at 450K.
There are 16 torsion angles in C19 molecule, which are denoted in turn. Figure 9 shows the final conformation of 79C19/GRA at 450K. Five typical C19 molecules are selected to study, which denoted by A (blue), B (orange), C (green), D (purple) and E (red). It can be seen that C19 A is extended, C19 B and C fold into two stems, C19 D occurs a non-integer fold, and C19 E folds into three stems. The torsion angles of C19 A, B, C, D and E at 10,000ps NVT MD simulations at 450K are listed in Table 1. The negative values of torsion angles in the Table 1 are shown as their absolute value.
Torsion angles of C19 A are all bigger than 150°, which indicates that C19 A is extended on graphene surface. There are fold and extended regions in the fold C19 molecules (B, C, D and E). The extended region is trans conformation. The torsion angles 1 ~ 6, 12 ~ 16 of C19 B, 2 ~ 7, 13 ~ 16 of C19 C, 1 ~ 8 of C19 D are about 170°. The conformation of the fold region is the gauche-gauche-trans-gauche-gauche or gauche-gauche-trans-gauche. This is similar with the structure of chain fold in the polyethylene [25, 57]. The torsion angles 7 ~ 11 of C19 B, 8 ~ 12 of C19 C, 9 ~ 12 of C19 D are in the fold regions. C19 E folds into three stems in Fig. 9. Torsion angles 2, 3, 5, 6, 8, 11, 12, 15 of C19 E are all less than 100°, indicating that C19 E twists heavily.
Liu et al. [33] found more detailed information of chain fold during n-alkane orientation from the evolution of the end-to-end distance. The change of C19 can be found from the time evolution of Red. The time evolution of the Red of C19 A, B, C, D and E at 450K are also shown in Fig. 10. The C19 A are curved at the beginning of the simulation and changes to extended conformation after 2000ps. The C19 B is bent from 1900ps to 8000ps and then folds into two stems again after 8000ps. The C19 C happens to fold before 2000ps and folds into two stems from 2000 to 10000ps. The C19 D folds into two stems at 5000ps and changes to a non-integer fold at the end of simulation. The C19 E twists at about 600 and 3200ps and fold into two stems at 4000ps. The C19 E folds into three stems finally.
When the conformation of n-alkane chain changes, the backbone torsion angles will change correspondingly. We choose three typical backbone torsion angles 1, 6, 8 of C19 B, which are at the end of chain, in the extended stem and in the fold region of the molecule after 10,000 NVT MD simulations, respectively. Figure 11 shows the evolutions of torsion angles 1, 6, 8 of C19 B on graphene surface during MD simulation at 450 K.
Three torsion angles fluctuate between 20° and 180° during C19 B twisting. The C19 B bends after 1900ps. Torsion angle 6 fluctuates between 150° and 180° from 1900ps to 4700ps, meaning that torsion angle 6 is in the extended stem. Torsion angles 1 and 8 fluctuate wildly from 1900ps to 4700ps. In the simulated time of 4700ps ~ 8000ps, torsion angles 1 and 6 fluctuate between 150° and 180°, meaning that they are in the extended stem. Torsion angle 8 fluctuates between 40° and 80°, meaning that torsion angle 8 is in the fold region. C19 B happens to fold at 8000ps and folds into two stems from 8000 to 10000ps again. Three torsion angles don’t change much after 8000ps. And torsion angles 1 and 6 are in the extended stem and torsion angle 8 is in the fold region.
When n-alkane chain fold occurs, torsion angle may move back and forth in the fold region and the extended stem. Some torsion angles in the fold region usually change to gauche conformation, and others in the extended stem usually adopt trans conformation. After the occurrence of chain fold, torsion angles fluctuate. Torsion angles in the fold region fluctuate stronger than that in the extended stem.
3.5. The Effect of the Interaction Energy on the Orientation
In this section, we will explore the effect of the interaction energy on the orientation of n-alkane with different chain lengths on graphene surface. We calculate the interaction energy between n-alkane chain (Echain), the interaction energy between molecule and graphene surface (Eint).
Eint = Etotal -(Echain + Eplane) (3)
where Etotal is total energy of the system, Eplane is energy of graphene surface. Figure 12 shows the variation of Eint, Echain and Eint-Echain for 115C13/GRA, 79C19/GRA and 60C25/GRA with increasing temperature.
For 115C13/GRA, Eint changes little as the temperature increases. Echain decreases from 300 to 450K and increases from 450 to 500K quickly. Eint is bigger than Echain at 300K, and Eint-Echain is about 2000kcal/mol. C13 molecules are disordered on the surface. This is due to n-alkane relaxing slowly at low temperatures. Echain are much lower than Eint, and Eint-Echain is about 4000kcal/mol from 370 to 490K. C13 molecules are perpendicular to graphene surface in this temperature range. Echain is as much as Eint at 500K when C13 molecules form a disordered structure.
For 79C19/GRA, Echain is lower than Eint, and Eint-Echain is about 2000kcal/mol at 300K. C19 molecules are disordered on the surface because n-alkane relaxes slowly. Echain decreases and Eint increases slowly from 300 to 480K. In addition, Echain is much lower than Eint, and Eint-Echain increases to about 3000kcal/mol gradually. C19 molecules tend to adopt perpendicular orientation on surface. When the temperature above 480K, Echain increases and Eint decreases suddenly. Echain is lower than Eint and Eint-Echain decreases to about 2000kcal/mol at 490K. C19 molecules form parallel ordered structure on the surface at 490K. Echain is close to Eint and Eint-Echain is about 500kcal/mol at 500K. C19 molecules form disordered structure on the surface.
For 60C25/GRA, Echain decreases from 300 to 480K, increases after 480K quickly. Eint changes little from 300 to 480K, decreases after 480K suddenly, and increases from 500 to 550K. A disordered structure form on the surface at 300K owing to n-alkane relaxes slowly. And Eint-Echain fluctuates around 2000kcal/mol, C25 molecules are parallel to the surface in the temperature range of 400 ~ 500K. C25 molecules form a disordered structure on the surface at 550K when Echain is close to Eint and Eint-Echain is about 500kcal/mol.
It is found that the ordered structure of n-alkanes is governed by Eint and Echain. When Eint-Echain is high enough at relative high temperature, n-alkanes can form ordered structure on graphene surface. Molecules are perpendicular to the surface when Eint-Echain of C13 molecules is about 4000kcal/mol. C19 and C25 molecules are parallel to the surface when Eint-Echain is about 2000kcal/mol. Although Eint-Echain is about 2000kcal/mol at low temperatures, C13, C19, C25 molecules are disordered on the surface. It's because n-alkane molecule relaxes slowly at low temperatures. When Eint-Echain is about 500kcal/mol at high temperatures, three kinds of n-alkanes form disordered structure. Eint-Echain of parallel ordered structure is much lower than that of perpendicular ordered structure. And Eint-Echain of disordered structure is lower than that of parallel ordered structure on the surface. This is consistent with the results of previous studies [46, 47, 58]. However, C19 molecules form perpendicular ordered structure when Eint-Echain is less than 4000kcal/mol because of chain fold.
As the simulation temperature changes, Eint and Echain change correspondingly and n-alkane molecules form different orientation structures. The difference between Eint and Echain of ten kinds of n-alkane molecules on graphene surface at different temperatures are shown in table S1 of the Supporting Information. Only when Eint-Echain is high enough, n-alkane molecules can form ordered structure on graphene surface. In addition, even if Eint-Echain is high, the ordered structure can’t form when the temperature is too low. When Eint-Echain is about 4000kcal/mol, short n-alkanes are perpendicular to the surface. When Eint-Echain is about 2000kcal/mol, n-alkanes are parallel to the surface. But when long n-alkanes form perpendicular ordered structure on the surface, Eint-Echain is less than 4000kcal/mol due to chain fold. When Eint-Echain is small, n-alkanes are disordered on the surface.
In this paper, we discuss the isothermal orientation process of ten kinds of n-alkane molecules on graphene surface at different temperatures in detail. We find that n-alkanes can form disordered structure, perpendicular ordered structure, parallel multi-layer structure on graphene surface. The longest n-alkane chain that forms perpendicular orientation is C16. The shortest n-alkane chain that forms parallel multi-layer ordered structure is C20. C17, C18 and C19 chains arrange perpendicularly to the graphene surface at relative low temperature and form parallel multi-layer structure at relative high temperature. When temperature is too low or high enough, the n-alkanes form disordered structures on graphene surface. It is also found that chain fold happens for long n-alkanes in perpendicular ordered structure. Due to the occurrence of chain fold, the height of the perpendicular ordered regions are smaller than the extended molecule. In addition, the formation process of fold chain is described by torsion angle and Red. When annealing procedures are performed on the system, the orientation of C18 molecules are irreversible with temperature. The C18 molecules are favorite forming perpendicular orientation at fast cooling rate and parallel orientation at slow cooling rate. Only one orientation appears for C18 during the annealing procedure. The parallel and perpendicular orientation can both obtained by isothermal MD simulations at different temperatures.
The chain length and simulation temperature play important role in the orientation of n-alkanes on graphene surface. The ordered structure of n-alkanes depends on the interactions of n-alkane-graphene (Eint) and n-alkane-n-alkane(Echain). When Eint-Echain is relatively strong enough, n-alkanes form ordered structure on graphene surface. But the ordered structure can’t form at low temperature even if Eint-Echain is high. The n-alkanes relaxes slowly at low temperature. When Eint-Echain is high, perpendicular ordered structure form on graphene surface. When Eint-Echain is low, parallel ordered structure form on graphene surface. The chain fold leads to lower Eint-Echain for long n-alkanes in perpendicular ordered structure. When Eint is close to Echain, n-alkane molecules form a disordered structure on the surface.
Our simulations give valuable insights into the mechanism of the two kinds of orientation formations of the n-alkanes adsorbed on graphene surface at different simulation temperatures, which is difficult to reveal experimentally, especially at atomic-scale description the orientation. The surface coverage is important during the orientation of n-alkanes on graphene surface. More research is needed to further investigate the influence of the surface coverage on the orientation in the future.
Funding: This work is supported by the Natural Science Foundation of Tianjin [no. 18JCYBJC90000] and the Science&Technology Development Fund of Tianjin Education Commission for Higher Education [2020KJ008].
Conflicts of interest/Competing interests: The authors declare no conflict of interest.
Availability of data and material: All raw data are available from the authors upon request.
Code availability: N/A
Authors' contributions: All the authors contributed to the design and implementation of the research, analyzed, revised the results and wrote the manuscript. Zhi Meng Zhang, Hua Yang, Jun Xia Shi and Hui Zhang did the calculations of the original manuscript. Zheng Guo Huang and Jia Jun Wang performed the simulations of the revised manuscript.
- Shan B, Miao Q (2017) Molecular design of n-type organic semiconductors for high-performance thin film transistors. Tetrahedron Lett 58:1903–1911
- Fortunato E, Barquinha P, Martins R (2012) Oxide semiconductor thin-film transistors: a review of recent advances. Adv Mater 24:2945–2986
- Cheng P, Li G, Zhan XW, Yang Y (2018) Next-generation organic photovoltaics based on non-fullerene acceptors. Nat Photon 12:131–142
- Yan H, Chen ZH, Zheng Y, Newman C, Quinn JR, Dötz F, Kastler M, Facchetti A (2009) A high-mobility electron-transporting polymer for printed transistors. Nature 457:679–686
- Yamamoto T, Nozaki K, Yamaguchi A, Urakami N (2007) Molecular simulation of crystallization in n-alkane ultrathin films: effects of film thickness and substrate attraction. J Chem Phys 127:154704
- Wang Y, Chan CM, Ng KM, Li L (2008) What controls the lamellar orientation at surface of polymer films during crystallization? Macromolecules 41:2548–2553
- Rissanou AN, Harmandaris V (2015) Structural and dynamical properties of polystyrene thin films supported by multiple graphene layers. Macromolecules 48:2761–2772
- Ma Y, Hu WB, Reiter G (2006) Lamellar crystal orientations biased by crystallization kinetics in polymer thin films. Macromolecules 39:5159–5164
- Fu J, Urquhart SG (2007) Effect of chain length and substrate temperature on the growth and morphology of n-alkane thin films. Langmuir 23:2615–2622
- Ueda Y, Ashida M (1980) The structure of n-hexatriacontane film vacuum-deposited on alkali halide crystals and its transformation by heat treatment. J Electron Microsc 29:38–44
- Masnadi M, Urquhart SG (2012) Effect of substrate temperature on the epitaxial growth of oriented n-alkane thin films on graphite. Langmuir 28:12493–12501
- Masnadi M, Urquhart SG (2013) Indirect molecular epitaxy: deposition of n-alkane thin films on Au coated NaCl(001) and HOPG(0001) surfaces. Langmuir 29:6302–6307
- Hooks DE, Fritz T, Ward MD (2001) Epitaxy and molecular organization on solid substrates. Adv Mater 13:227–241
- Nozaki K, Saihara R, Ishikawa K, Yamamoto T (2007) Structure of normal alkane evaporated films: molecular orientation. Jap J Appl Phys 46:761–769
- Kubono A, Yuasa N, Shao HL, Umemoto S, Okui N (2002) Adsorption characteristics of organic long chain molecules during physical vapor deposition. Appl Surf Sci 193:195–203
- Kubono A, Minagawa Y, Ito T (2013) In situ study on layer-by-layer growth in vapor deposition of linear long-chain molecules using a quartz crystal microbalance. J Appl Phys 114:38
- Fukao K, Horiuchi T, Matsushige K (1989) Observation of molecular orientation in evaporated films of n-paraffins. Thin Solid Films 171:359–366
- Vácha R, Roke S (2012) Sodium dodecyl sulfate at water – hydrophobic interfaces: a simulation study. J Phys Chem B 116:11936–11942
- Bresme F, Chacón E, Tarazona P, Tay K (2008) Intrinsic structure of hydrophobic surfaces: the oil-water interface. Phys Rev Lett 101:1–4
- Hantal G, Partay L, Varga I, Jedlovszky P, Gilányi T (2007) Counterion and surface density dependence of the adsorption layer of ionic surfactants at the vapor-aqueous solution interface: a computer simulation study. J Phys Chem B 111:1769–1774
- Popov P, Steinkerchner L, Mann EK (2015) Molecular dynamics study of rhodamine 6G diffusion at n-decane-water interfaces. Phys Rev E 91:053308
- Qiu YQ, Molinero V (2017) Strength of alkane-fluid attraction determines the interfacial orientation of liquid alkanes and their crystallization through heterogeneous or homogeneous mechanisms. Crystals 7:86
- Haas FM, Hilfer R, Binder K (1995) Layers of semiflexible chain molecules endgrafted at interfaces: an off-lattice Monte Carlo simulation. J Chem Phys 102:2960
- Wang SJ, Hong YL, Yuan SC, Chen W, Zhou WX, Li Z, Wang K, Min X, Konishi T, Miyoshi T (2018) Chain trajectory, chain packing, and molecular dynamics of semicrystalline polymers as studied by solid-state NMR. Polymers 10:775
- Ungar G, Zeng XB (2001) Learning polymer crystallization with the aid of linear, branched and cyclic model compounds. Chem Rev 101:4157–4188
- Ungar G, Zeng XB, Spells SJ (2000) Non-integer and mixed integer forms in long n-alkanes observed by real-time LAM spectroscopy and SAXS. Polymer 41:8775–8780
- Hobbs JK, Hill MJ, Barham PJ (2000) Isothermal thickening of single crystals of C294H590 in dilute solution. Polymer 41:8761–8773
- Iwata M, Sato H (1999) Chain movement in crystallization process by molecular dynamics simulation. Phys Chem Chem Phys 1:2491–2500
- Fujiwara S, Sato T (2001) Molecular dynamics study of structure formation of a single polymer chain by cooling. Comput Phys Commun 142:123–126
- Fujiwara S, Sato T (2002) Molecular dynamics simulation of a single polymer chain in vacuum and in solution. Comput Phys Commun 147:342–345
- Kavassalis TA, Sundararajan PR (1993) A molecular dynamics study of polyethylene crystallization. Macromolecules 26:4144–4150
- Shakirov T, Paul W (2019) Folded alkane chains and the emergence of the lamellar crystal. J Chem Phys 150:084903
- Liu YF, Yang H, Zhang H (2018) Molecular dynamics simulation of the folding of single alkane chains with different lengths on single-walled carbon nanotubes and graphene. J Mol Model 24:140
- Gulde M, Rissanou AN, Harmandaris V, Muller M, Schafer S, Ropers C (2016) Dynamics and structure of monolayer polymer crystallites on graphene. Nano Lett 16:6994–7000
- Ma ZW, Yang P, Zhang XY, Jiang K, Song Y, Zhang WK (2019) Quantifying the chain folding in polymer single crystals by single-molecule force spectroscopy. Acs Macro Lett 8:1194–1199
- Tracz A, Kucinska I, Jeszka JK (2003) Formation of highly ordered, unusually broad polyethylene lamellae in contact with atomically flat solid surfaces. Macromolecules 36:10130–10132
- Tracz A, Jeszka JK, Kucinska I, Chapel JP, Boiteux G, Kryszewski M (2002) Influence of the crystallization conditions on the morphology of the contact layer of polyethylene crystallized on graphite: atomic force microscopy studies. J Appl Polym Sci 86:1329–1336
- Novoselov KS, Geim AK, Morozov SV, Jiang D, Zhang Y, Dubonos SV, Grigorieva IV, Firsov AA (2004) Electric field effect in atomically thin carbon films. Science 306:666–669
- Geim AK (2009) Graphene: status and prospects. Science 324:1530–1534
- Kumar S (2018) Graphene engendered aluminium crystal growth and mechanical properties of its composite: an atomistic investigation. Mater Chem Phys 208:41–48
- Endo O, Nakamura M, Amemiya K, Ozaki H (2019) Thermal dehydrogenation of n-alkane on Au(111) and Pt(111) surface. Surf Sci 681:32–37
- Idowu A, Boesl B, Agarwal A (2018) 3D graphene foam-reinforced polymer composites–a review. Carbon 135:52–71
- Verma A, Parashar A, Packirisamy M (2019) Effect of grain boundaries on the interfacial behaviour of graphene-polyethylene nanocomposite. Appl Surf Sci 470:1085–1092
- Devi JM (2019) Simulation of graphene–fullerene nanohybrid structure. B Mater Sci 42:75
- Kim K, Santos EJG, Lee TH, Nishi Y, Bao ZA (2015) Epitaxially grown strained pentacene thin film on graphene membrane. Small 11:2037–2043
- Yang H, Liu YF, Zhang H (2018) Fully atomistic molecular dynamics simulations of the isothermal orientation of n-decanes confined between graphene sheets. J Phys Chem C 122:26226–26235
- Liu YF, Yang H, Zhang ZM, Zhang H (2019) Molecular dynamics simulations on the orientation of n-alkanes with different lengths on graphene. Surf Sci 690:121468
- Sun H (1995) Ab initio calculations and force field development for computer simulation of polysilanes. Macromolecules 28:701–712
- Sun H (1998) COMPASS: An ab initio force-field optimized for condensed-phase applications-overview with details on alkane and benzene compounds. J Phys Chem B 102:7338–7364
- Sun H, Ren P, Fried JR (1998) The COMPASS force field: parameterization and validation for phosphazenes. Comput Theor Polym S 8:229–246
- Nikkhah SJ, Moghbeli MR, Hashemianzadeh SM (2016) Dynamic study of deformation and adhesion of an amorphous polyethylene/graphene interface: a simulation study. Macromol Theor Simul 25:533–549
- Sutay B, Yurtsever M (2017) Adsorption of dihalogen molecules on pristine graphene surface: Monte Carlo and molecular dynamics simulation studies. J Mol Model 23:150
- Zhao XT, Yang H, Sheng YZ, Li JY, Sun M (2014) Molecular dynamics simulation on the effect of the distance between SWCNTs for short polymers diffusion among single wall carbon nanotubes. Comp Mater Sci 95:446–450
- Nosé S (1984) A unified formulation of the constant temperature molecular dynamics methods. J Chem Phys 81:511–519
- Nosé S (1984) A molecular dynamics method for simulations in the canonical ensemble. Mol Phys 52:255–268
- Nosé S (1991) Constant temperature molecular dynamics methods. Prog Theor Phys Supp 103:1–46
- Kay HF, Newman BA (1968) The crystal and molecular structure of cyclotetratriacontane [CH2]34. Acta Crystallogr Sect B B24:615–624
- Wang XL, Lu ZY, Li ZS, Sun CC (2007) Molecular dynamics simulation study on controlling the adsorption behavior of polyethylene by fine tuning the surface nanodecoration of graphite. Langmuir 23:802–808
- SupportingInformationJMMOD2000623.docx
Supporting Information