# The effect of uniaxial strain on graphene nanoribbon carrier statistic

- Zaharah Johari
^{1}and - Razali Ismail
^{1}Email author

**8**:479

https://doi.org/10.1186/1556-276X-8-479

© Johari and Ismail; licensee Springer. 2013

**Received: **18 July 2013

**Accepted: **11 October 2013

**Published: **14 November 2013

## Abstract

Armchair graphene nanoribbon (AGNR) for *n*=3*m* and *n*=3*m*+1 family carrier statistic under uniaxial strain is studied by means of an analytical model based on tight binding approximation. The uniaxial strain of AGNR carrier statistic models includes the density of state, carrier concentration, and carrier velocity. From the simulation, it is found that AGNR carrier concentration has not been influenced by the uniaxial strain at low normalized Fermi energy for *n*=3*m* and *n*=3*m*+1. In addition, the carrier velocity of AGNR is mostly affected by strain at high concentration of *n*≈3.0×10^{7} and 1.0 × 10^{7} m^{−1} for *n*=3*m* and *n*=3*m*+1, respectively. The result obtained gives physical insight into the understanding of uniaxial strain in AGNR.

### Keywords

GNR Uniaxial strain Carrier statistic## Background

Graphene has attracted numerous research attention since it was isolated in 2004 by Novoselov et al. [1]. Due to its unique hexagonal symmetry, graphene posses many remarkable electrical and physical properties desirable in electronic devices. It is the nature of graphene that it does not have a bandgap, which has limited its usage. Therefore, efforts to open up a bandgap has been done by several methods [2–4]. The most widely implemented method is patterning the graphene into a narrow ribbon called graphene nanoribbon (GNR) [4]. Recently, strain engineering have started to emerge in graphene electronics [5]. It is found that strain applied to graphene can modify its band structure, thus, altering its electronic properties [6–8]. In fact, uniaxial strain also helps in improving the graphene device’s electrical performance [9]. Similar characteristics have been observed when strain is applied to conventional materials like silicon (Si), germanium (Ge), and silicon germanium (SiGe) [10]. Strain in graphene can be characterized by two major varieties, namely uniaxial and shear. This strain behaves differently on graphene depending on the edge shape, namely zigzag or armchair [8]. The presence of the strain effect in graphene is by the *G* peak that splits and shifts in the Raman spectrum [11, 12]. It is worth noting that strain in graphene may unintentionally be induced during the fabrication of graphene devices.

Computational modeling and simulation study pertaining to strain graphene and GNR for both the physical and electrical properties have been done using few approaches such as the tight binding model and the ab initio calculation [6, 13]. An analytical modeling approach has also been implemented to investigate the strain effect on GNR around the low-energy limit region [14, 15]. However, most of the previous works have only focused on the electronic band structure, particularly the bandgap. As the carrier transport in GNR has a strong relation with this electronic band structure and bandgap, it is mandatory to investigate the strain effect on the carrier transport such as carrier density and velocity. Therefore, in this paper, an analytical model representing uniaxial strain GNR carrier statistic is derived based on the energy band structure established by Mei et al. [15]. The strain effect in our model is limited to low strain, and only the first subband of the AGNR *n*=3*m* and *n*=3*m*+1 families is considered. In the following section, the analytical modeling of the uniaxial strain AGNR model is presented.

## Methods

### Uniaxial strain AGNR model

*p*

_{ z }orbitals that form the

*π*bands when the lattice constant changes [6]:

where ${t}_{1}=\frac{{t}_{0}}{{\left(1+\epsilon \right)}^{2}}$, ${t}_{2}={t}_{3}=\frac{{t}_{0}}{\left(1+\frac{\epsilon}{4}\right)}$, *t*_{0}=−2.74 eV is the unstrained hopping parameter, *a*=0.142 nm is the lattice constant and *t*_{1} and *t*_{2} are the deformed lattice vector hopping parameter of the strained AGNR. *ε* is the uniaxial strain [15].

*k*

_{ x }=0, Equation 2 is reduced to [15]

*v*

_{ f }, is modeled as in reference [18]. Thus,

*v*

_{ f }is obtained as the following equation:

The analytical model presented in this section is plotted and discussed in the following section.

## Results and discussion

*k*

_{ x }, modeled as in Equation 1 which was established by Mei et al. [15], is plotted in Figure 1 for

*n*=3

*m*and

*n*=3

*m*+1 family, respectively. For each simulation, only low strain is tested since it is possible to obtain experimentally [12]. It can be observed from both figures that there is a distinct behavior between the two families. For

*n*=3

*m*, the separation between the conduction and valence bands, which is also known as bandgap, increases with the increment of uniaxial strain. On the contrary, the

*n*=3

*m*+1 family exhibits decrements in the separation of the two bands. It is worth noting that the

*n*=3

*m*+1 family also shows a phase metal-semiconductor transition where at 7% of strain strength, the separation of the conduction and valence bands almost crosses at the Dirac point. This is not observed in the

*n*=3

*m*family [15].

The hopping integral *t*_{0} between the *π* orbitals of AGNR is altered upon strain. This causes the up and down shift, the *σ*^{∗} band, to the Fermi level, *E*_{
F
}[19]. These two phenomena are responsible for the bandgap variation. It has been demonstrated that GNR bandgap effect with strain is in a zigzag pattern [14]. This observation can be understood by the shifting of the Dirac point perpendicular to the allowed *k* lines in the graphene band structure and makes some bands closer to the Fermi level [7, 8]. Hence, the energy gap reaches its maximum when the Dirac point lies in between the two neighboring *k* lines. The allowed *k* lines of the two families of the AGNR have different crossing situations at the *K* point [8]. This may explain the different behaviors observed between *n*=3*m* and *n*=3*m*+1 family.

*n*=3

*m*family is inversely proportional to the GNR width. The narrow bandgap at the wider GNR width is due to the weaker confinement [20]. The conventional material of Si and Ge bandgaps are also plotted in Figure 2 for comparison. In order to achieve the amount of bandgap similar to that of Si (1.12 eV) or Ge (0.67 eV), the uniaxial strain is projected to approximately 3% for the

*n*=3

*m*family. A similar observation can be seen for

*n*=3

*m*+1 with 2% uniaxial strain. However, a higher strain resulted in a different kind of observation. For example at 4% uniaxial strain, the phase transition from metallic to semiconductor occurs at a GNR width of approximately 3

*m*. The phase transition is not observed in AGNR

*n*=3

*m*[15]. When higher strain is applied, the phase transition occurs at a lower width. The difference in GNR width for the phase transition to occur depends on the subband spacing effect with GNR width [21]. The constitution of the phase transition suggests that the GNR bandgap can be tuned continuously between the metal and semiconductor by applying strain.

*n*=3

*m*, the increment of strain increases the DOS remarkably. However, when

*ε*=3

*%*, despite the wide bandgap, the DOS substantially decreases. This is the reason for changing the band index,

*p*, which corresponds to the bandgap [15]. In the case of

*n*=3

*m*+1, the DOS exhibits the opposite. In fact, when the strain strength made the band approach the transition phase, the DOS reduces significantly; at the same time, the bandgap approaches zero.

*η*is shown in Figure 4. Apparently, the amount of carriers increases when the AGNR

*n*=3

*m*is added with uniaxial strain. Conversely, AGNR

*n*=3

*m*+1 shows a reduction in carrier concentration upon strain. Most notably, for AGNR

*n*=3

*m*, the carrier concentration converges at low

*η*within the investigated strain level. Meanwhile, the carrier concentration exhibits considerable effect upon the strain when the Fermi level lies at 3

*k*

_{ B }T away from the conduction or valence band edge. The same observation was achieve in AGNR

*n*=3

*m*+1.

*n*=3

*m*and AGNR

*n*=3

*m*+1 families, respectively. Inspection of these figures also showed that the uniaxial strain mostly affected the carriers at high concentration. This is evident by the curves that tend to converge until

*n*≈3×10

^{7}m

^{−1}and has an almost constant velocity at 1.8 × 10

^{5}ms

^{−1}. When the concentration is high enough, the uniaxial strain starts to give a considerable effect to the velocity. This is supported by the previous observation in Figure 4 where the effect of the strain is infinitesimal at low

*η*. In fact, the applied strain also affects the degeneracy approach. The strained AGNR

*n*=3

*m*approach degenerated later compared to the unstrained AGNR. A similar behavior was also observed in the AGNR

*n*=3

*m*+ 1 family except that strained AGNR approaches degeneracy faster compared to their unstrained counterparts. This indicates that uniaxial strain is beneficial at a high concentration regime. Nonetheless, this is not unreasonable for low-dimensional nanostructures like GNR since it is mostly in the degenerated realm particularly for narrow width.

*n*=3

*m*and

*n*=3

*m*+1 have appreciable reduction in the Fermi velocity when the uniaxial strain increases as can be seen in Figure 6a,b. This reduction is attributed to the decrements in the

*π*orbital overlap [22] in the AGNR band structure. As a consequence, the mobility is predicted to be degraded [23] as a result of the strong effect in the interaction of the strained carbon atoms [18, 23].

## Conclusions

In this paper, the uniaxial strain AGNR for *n*=3*m* and *n*=3*m* + 1 family carrier statistic is analytically modeled, and their behaviors are studied. It is found that uniaxial strain gives a substantial effect to AGNR carrier statistic within the two AGNR families. The AGNR carrier concentration has not been influenced by the uniaxial strain at low normalized Fermi energy. It is also shown that the uniaxial strain mostly affects carrier velocity at a high concentration of *n*≈3.0×10^{7} m ^{−1} and *n*≈1.0×10^{7} m ^{−1} for *n*=3*m* and *n*=3*m*+1, respectively. In addition, the Fermi velocity of the AGNR *n*=3*m* and *n*=3*m*+1 exhibits decrements upon the strain. Results obtained give physical insight on the understanding of the uniaxial strain effect on AGNR. The developed model in this paper representing uniaxial strain AGNR carrier statistic can be used to further derive the current-voltage characteristic. This computational work will stimulate experimental efforts to confirm the finding.

## Declarations

### Acknowledgements

The authors would like to acknowledge the financial support from the Research University grant of the Ministry of Higher Education (MOHE), Malaysia under project number R.J130000.7823.4F146. Also, thanks to the Research Management Centre (RMC) of Universiti Teknologi Malaysia (UTM) for providing excellent research environment in which to complete this work.

## Authors’ Affiliations

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