# Nanoindentation experiments for single-layer rectangular graphene films: a molecular dynamics study

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- Received:
- Accepted:

DOI: 10.1186/1556-276X-9-41

- Cite this article as:
- Wang, W., Li, S., Min, J. et al. Nanoscale Res Lett (2014) 9: 41. doi:10.1186/1556-276X-9-41

## Abstract

A molecular dynamics study on nanoindentation experiments is carried out for some single-layer rectangular graphene films with four edges clamped. Typical load–displacement curves are obtained, and the effects of various factors including indenter radii, loading speeds, and aspect ratios of the graphene film on the simulation results are discussed. A formula describing the relationship between the load and indentation depth is obtained according to the molecular dynamics simulation results. Young’s modulus and the strength of the single-layer graphene film are measured as about 1.0 TPa and 200 GPa, respectively. It is found that the graphene film ruptured in the central point at a critical indentation depth. The deformation mechanisms and dislocation activities are discussed in detail during the loading-unloading-reloading process. It is observed from the simulation results that once the loading speed is larger than the critical loading speed, the maximum force exerted on the graphene film increases and the critical indentation depth decreases with the increase of the loading speed.

### Keywords

Molecular dynamics simulation Nanoindentation Rectangular graphene film Young’s modulus Strength### Abbreviations

- 2-D
two-dimensional

- AFM
atomic force microscope

- AIREBO
adaptive intermolecular reactive empirical bond order

- GPa
gigapascals

- MD
molecular dynamics

- NVT
constant number of particles, volume, and temperature

- SW
Stone-Wales 5-7-7-5

- TPa
terapascals.

## Background

The perfect graphene is a kind of carbonaceous material which consists of two-dimensional honeycomb lattice structures of single layer of carbon atoms. It is the basic unit to build other dimensional carbonaceous materials, such as zero-dimensional fullerenes, one-dimensional carbon nanotubes, and three-dimensional graphite[1, 2]. Graphene sheets/ribbons/films have attracted the interest of the scientific community because of recent exciting experimental results[3, 4, 5, 6]. Their growth, atomic makeup, electronics, doping, and intercalation have attracted many investigations[7, 8, 9, 10]. A suspended graphene sheet[1, 11] can be used in a variety of ways, such as for pressure sensors or gas detectors[12] or mechanical resonators[13].

It is still debatable whether a graphene sheet is truly a two-dimensional structure or if it should be regarded as a three-dimensional structure since it exhibits a natural tendency to ripple, as observed in recent experiments[2, 14, 15, 16]. Carlsson addressed that an understanding of the coupling behaviors between bending and stretching of graphene sheets is necessary to fully explain the intrinsic ripples in a graphene sheet[15]. In addition to theoretical investigations, recent research has been carried out to measure the mechanical properties of suspended graphene sheets by utilizing an atomic force microscope (AFM)[17]. Through weak van der Waals forces, graphene sheets were suspended over silicon dioxide cavities where an AFM tip was probed to test its mechanical properties. Their Young’s modulus differs from that of bulk graphite. Poot and van der Zan[18] measured the nanomechanical properties of graphene sheets suspended over circular holes by using an AFM and suggested that graphene sheets can sustain very large bending and stretching prior to the occurrence of fracture, which indicates that the classical Kirchhoff plate theory used in the bending and vibration analysis of graphene sheets may not be suitable since deflection and stretching are considerable[19]. Some researchers thought that the large deflection plate theory of von Kármán may be a better candidate to model the graphene sheet, and they have characterized its bending and stretching through that theory[20, 21]. Lee et al. measured Young’s modulus and the maximum stress of graphene by using an AFM in the nanoindentation experiment[22] and reported the effect of grain boundaries on the measurement of chemical vapor-deposited graphene[23]. Fang et al.[24] has studied the mechanical behavior of a rectangular graphene film under various indentation depths, velocities, and temperatures using molecular dynamics (MD) simulations. The physical models of the rectangular graphene film established by Fang et al. are doubly clamped using a bridge-type support and are loaded by a flat-bottomed diamond tip.

Although the above research has been carried out for mechanical properties of graphene, the variation of the values of elastic modulus has not yet reached a consensus. Especially for rectangular graphene films, the relationship between the load and the indentation depth is not clear. Furthermore, there are few papers available which describe the deformation mechanisms and dislocation activities of graphene film during the nanoindentation processes in detail. These investigations are concentrated on tension deformation[25, 26, 27, 28] and shear deformation[29]. Almost all of the available literatures on dislocation activities in graphene focus on theoretical studies and numerical simulations, including density functional theory (DFT)[26], tight-binding molecular dynamics (TBMD)[30], *ab initio* total energy calculation[30], and quantum mechanical computations[31]. Researchers always artificially applied defects or dislocations and then studied their effects on the properties and activities in graphene. However, due to the bottleneck of experimental study at nanoscale, a very few experimental observations of dislocation activities are available at present. Warner et al.[32] also reported the observation of dislocation pairs through HRTEM experiments and gave five possible mechanisms that describe how these dislocation pairs could have formed, namely, during the CVD growth, electron beam sputtering of carbon dimers along a zigzag lattice direction, from surface adatom incorporation, from a monovacancy, and from a Stone-Wales defect. They then concluded that edge dislocations result in substantial deformation of the atomic structure of graphene, with bond compression or elongation of ±27%, plus shear strain and lattice rotations.

In this article, some MD simulations of nanoindentation experiments are performed on a set of single-layer rectangular graphene films with four clamped edges. The dislocation activities and the deformation mechanism are discussed, and a formula is introduced in order to describe the relationship of load and indentation depth and to measure the mechanical properties of graphene.

## Methods

When performing MD simulations, we use the canonical (i.e., NVT) ensemble and control the temperatures at an ideal temperature of 0.01 K. In order to avoid the complex effects of the atomic thermal fluctuations, the temperature is regulated with the Nosé-Hoover method and the time step was set to 1 fs. During the simulation, one key step, named energy minimization and relaxation, should be carried out to make the system remain in the equilibrium state with lowest energy. Then, the indentation experiment was executed and the simulation results were output for further research.

## Results and discussion

### Loading and unloading properties

We take the case of the graphene film with an aspect ratio of 1.2 and the diamond indenter with a radius of 2 nm as an example to describe the indentation experiment in the following. The indenter was placed over the geometric center of the graphene film and forced to move in the direction perpendicular to the original graphene surface. Figure 1 gives the atomic configurations of the system model during the indentation experiment at a speed of 0.20 Å/ps. The atoms on the edge of the graphene film remained in a static state due to fixed boundary conditions. After enough loading time, the graphene film is eventually pierced through by the indenter, appearing some fractured graphene lattices. The load–displacement curves can be attained from the data of intender load (*F*) and indentation depth (*d*) calculated in MD simulations. The moment the load–displacement curve drops suddenly is considered to be a critical moment. In our simulations, the load suddenly decreased once the indentation depth exceeded 5.595 nm, defined as the critical indentation depth (*d*_{c}), and the corresponding maximum load (*F*_{max}) is 655.08 nN.

Stage I. The unloading process is done before the indentation depth reaches the critical depth,

*d*_{c}. The graphene sheet almost can make a complete recovery, i.e., restore its initial structures, and the curves of reloading processes almost perfectly match the initial loading curve while the unloading curve shows very small deviations from the initial one, as shown in the inset of Figure 3. In general, the almost-perfect coincidence is due to the fact that the carbon covalent bonds and the graphene lattice structure are not destroyed. It can be concluded that there is no plastic deformation in this stage, i.e., the graphene undergoes elastic deformation.Stage II, i.e., the yellow region in Figure 3. In Figure 4a,b,c, it is after the indentation depth exceeded

*d*_{c}that the unloading process begins. The graphene sheet cannot make a complete recovery, and there exited broken covalent bonds after the unloading process. In the reloading process, the maximum force exerting on graphene is much smaller than that in Figure 3, which denotes the fracture of graphene lattices. Figure 4b describes the state where the unloading process begins, and Figure 4c describes the state where the unloading process ends. After the loading process, there exited broken bonds and fractured lattices in the middle of the graphene film and these defective structures did not recover during the unloading process. Therefore, the deformation of the graphene described in this figure can be considered as a plastic type.

### Young’s modulus and strength of the graphene film

*d*is the indentation depth and

*F*denotes the concentrated force gotten by the graphene film. In Equation 1, the load

*F*consists of two parts: the first part,

*F*

_{σ}(

*d*), represents the term due to the axial tension of the two-dimensional (2-D) film,

*σ*

_{0}

^{2D}is the pre-tension of the single-layer graphene film,

*r*is the indenter radius,

*β*denotes the aspect ratio and is equal to

*L*/

*b*, and

*R*

_{equ}represents the equivalent radius of the rectangular graphene sheet, (

*Lb*/

*π*)

^{1/2}. The second one,

*F*

_{E}(

*d*), represents the large deformation term,

where *E*^{2D} is the 2-D elastic modulus, i.e., Young’s modulus, of the single layer graphene film. The strain energy density of graphene, as a standard 2-D material, can be represented by the energy of per unit area. Then, the corresponding pre-tension and elastic modulus can be expressed as *σ*_{0}^{2D} and *E*^{2D}, respectively, with the unit N/m. The common pre-tension and elastic modulus of a 3-D bulk material can be obtained through these 2-D values divided respectively by the effective thickness which is always treated as the layer spacing of the graphite crystal, i.e., 3.35 Å. *q* is an nondimensional value, *q* = 1/(1.05 - 0.15*ν* - 0.16*ν*^{2}) = 0.9795, where *ν* denotes Poisson’s ratio, *ν* = 0.165[3, 18, 21]. It is reported that when *r*/*R* > 0.1, the indenter radius has a significant influence on the load–displacement properties[38, 39]. In our simulations, *r*/*R* > 0.1; thus, Equations 2 and 3 are corrected by a factor of (*r*/*R*)^{3/4} and (*r*/*R*)^{1/4}, respectively.

*ab initio*methods[41]. Lee et al. obtained a Young’s modulus of 1 ± 0.1 TPa by nanoindentation in an AFM of freestanding monolayer circular graphene membranes[22]. Neek-Amal and Peeters studied the nanoindentation of a bilayer graphene using molecular dynamics simulations and estimated a Young’s modulus of 0.8 TPa[42]. In addition, the maximum stress ranges from 130 to 240 GPa by means of both experiments and numerical simulations reported in other literatures[21, 22, 43, 44]. The maximum stress obtained in this paper can also be included in the above range, which verified our simulation results. The changing trend of 2-D pre-tension demonstrates that the pre-tension of the rectangular graphene film is positively correlated with the loading speed of the indenter. The indenter size also affects the pre-tension, which, to some extent, explains why the correction factors were introduced in Equations 2 and 3.

**Mechanical properties of the single-layer graphene film from nanoindentation experiments**

Indenter radius (Å)/speed (Å/ps) | 2-D elastic modulus (N/m) | 3-D elastic modulus (TPa) | 2-D pre-tension (N/m) | 3-D pre-tension (GPa) | 2-D max stress (N/m) | 3-D max stress (GPa) |
---|---|---|---|---|---|---|

10/0.10 | 375.0644 | 1.1196 | 38.8546 | 115.9840 | 72.4895 | 216.3866 |

10/0.20 | 375.0096 | 1.1194 | 38.8589 | 115.9966 | 72.4771 | 216.3496 |

20/0.10 | 335.0012 | 1.0000 | 28.5092 | 85.1021 | 66.1326 | 197.4106 |

20/0.20 | 335.2572 | 1.0008 | 28.4879 | 85.0385 | 66.0994 | 197.3115 |

30/0.10 | 349.1828 | 1.0423 | 22.7998 | 68.0590 | 67.4504 | 201.3445 |

30/0.20 | 348.8383 | 1.0413 | 23.0197 | 68.7154 | 67.6680 | 201.9940 |

Average | 353.0589 | 1.0539 | / | / | 68.7195 | 205.1328 |

### Other parameters’ influences on nanoindentation experiments

*F*

_{max}and

*d*

_{c}are not that obvious. When the loading speed decreases from 1.00 to 0.50 Å/ps, dropping by 50%, the value of

*d*

_{c}increases by 33.35%, and the value of

*F*

_{max}decreases by 8.43% correspondingly. Nevertheless, when the loading speed decreases from 0.20 to 0.10 Å/ps, dropping by 50%, the changes of

*F*

_{max}and

*d*

_{c}are only 1.68% and 0.21%, respectively. The results may be attributed to the fact that the higher the loading speed of the indenter, the less time it takes to go through the graphene sheet, resulting in a higher load and lower indentation depth than those at a lower loading speed, in which situation the load process is much slower. Secondarily, the spherical indenter’s influences on results are observed by changing the indenter radius. The simulations of various indenter radii (1, 2, and 3 nm) are carried out at the speed of 0.20 Å/ps. The results of the load–displacement curve are shown in Figure 6b. The stress is more uniform in the middle of the graphene, so the

*F*

_{max}increases obviously and the critical indentation depth also becomes greater with the increase of the indenter radius. Finally, after changing the aspect ratio of the graphene film to 1.1 and 1.5, Young’s modulus and the maximum stress of the graphene are obtained using the methods mentioned above. It can be deduced from Figure 7 that Young’s modulus and the maximum stress are the inherent properties of graphene and irrelevant to its size, which also verifies the formula obtained above.

## Conclusions

Some MD simulations of nanoindentation experiments on single-layer rectangular graphene sheets have been carried out in order to obtain the mechanical properties of graphene. A correlation between the load and the indentation depth is constructed, and Young’s modulus and the strength of graphene are obtained in the end. The simulation results show that the unloaded graphene film could make a complete recovery if the maximum indentation depth is less than the critical indentation depth, and the graphene film undergoes elastic deformation during the whole loading-unloading-reloading process. However, if the maximum indentation depth is larger than the critical indentation depth, the graphene sheet could not restore its original structures after unloading and the graphene deforms plastically. Based on the simulations of nanoindentation at different loading speeds and indenter radii, it can be observed that the maximum load increased and the critical indentation depth decreased with the increase of loading speed. In addition, the indenter radius has a remarkable influence on the force-displacement curve. As the indenter radius increases, the critical load and the critical indentation depth also increase.

## Acknowledgements

We acknowledge the financial support provided by the Fundamental Research Funds for the Natural Science Basic Research Plan in Shaanxi Province of China (grant no. 2013JM7017), subsequently by the National Natural Science Foundations of China (grant no. 51205302 and no. 50903017) and the Central Universities in Xidian University (grant no. K5051304006). We also would like to thank all the reviewers for their comments and kind suggestions to our manuscript and all the editors for their careful corrections on the final version of the article.

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