Scholarly article on topic 'Acoustic Phonons in Nanowires with Embedded Heterostructures'

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Academic research paper on topic "Acoustic Phonons in Nanowires with Embedded Heterostructures"

Hindawi Publishing Corporation Journal of Nanomaterials Volume 2011, Article ID 743846, 7 pages doi:10.1155/2011/743846

Research Article

Acoustic Phonons in Nanowires with Embedded Heterostructures

Hussein M. Ayedh1,2 and Andreas Wacker1

1 Mathematical Physics, Lund University, Box 118, 22100 Lund, Sweden

2 Physics Department, Faculty of Science, Thamar University, Box 87246, Dhamar, Yemen

Correspondence should be addressed to Andreas Wacker, Received 30 June 2011; Accepted 10 August 2011 Academic Editor: Raymond Whitby

Copyright © 2011 H. M. Ayedh and A. Wacker. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

Acoustic phonons are studied in finite nanowires based on the elastic continuum model. The phonon dispersion relations are compared for different types of approximations both for pure nanowires and nanowire heterostructures including cubic and wurtzite materials. We find that the isotropic approximation highly underestimates the frequency of torsional modes. The impact of heterostructures on the lowest modes is rather weak and can be described by an average of the different structure parameters.

1. Introduction

The phonon spectrum for semiconductor nanowires is important for a variety of applications. On the one hand, nanowires are of high interest for thermoelectric applications [1, 2], where the energy transport by phonons deteriorates the performance [3]. Furthermore, the phonon scattering is an important feature for all sorts of electronic devices [4]. This interaction could recently be directly experimentally accessed [5,6].

Currently, most calculations of the phonon spectrum are done either within the isotropic approximations for ideal (e.g., [7]) and coupled [8] quantum wires or using atomistic approaches (e.g., [3, 9]). Here, we present corresponding calculations using the commercial COMSOL package [10], which allows to treat both the correct cubic material properties and nanowires with embedded heterostructures in a straightforward way. This enables us to check the quality of the approximation by an isotropic material and the impact of heterostructures [11] on the acoustic branches, which is most important for the broadening of the zero photon line [12].

Our paper is organized as follows: in Section 2, we show how we extract the phonon dispersion relation from simulations of a finite nanowire length. Here, we consider the isotropic approximation, where one has easy access to analytical results for comparison. Section 3 focuses on the cubic

material properties of GaAs wires, where we analyze the differences for the acoustic branches. Nanowire heterostructures are considered in Section 4, where we show that the acoustic branches are only weakly affected. The application to wurtzite structures, see also [13], is demonstrated in Section 5.

2. Obtaining the Phonon Spectrum from Finite Nanowires

Throughout this work, we apply the elastic continuum model, which treats the crystal as a continuum. Thus, the internal vibrations that give rise to the optical modes cannot be considered in this model [14]. It is valid as long as the wavelength of the phonon mode is much longer than the lattice dimension.

The linear relation between stress T and strain S has the general form

Ti = X CijSj, (i = 1,2, ...,6). (1)

Here, cij are the elastic stiffness constants with 36 elements in Voigt notation. These stiffness constants can be reduced depending on the symmetries of the material. Many common semiconductors having diamond structure (e.g., silicon and germanium) or zincblende structure (e.g., GaAs and InAs)

exhibit cubic symmetry. The matrix of elastic constants for such materials has only three independent elements [15, 16], en, ci2, and C44.

For isotropic approximation these three independent elastic moduli for the cubic materials can be decreased into two moduli, and they have been expressed by Lamé constants X and p

X — C12,

_ (cil - C12)

Then, the elastic moduli matrix in the isotropic approximation will only include both of Lamé constants as distinct constants

2p + X X X 0 0 0"

X 2p + X X 000

X X 2p + X 000

0 0 0 p 0 0

0 0 0 0 p 0

0 0 0 0 0 p

As most of the materials have their elastic properties described in terms of Young's modulus E and Poissons ratio v [17], the two Lamé constants X and p can be written in terms of E and v [17]

(1 + v)(1 - 2v)' E

2(1 + v)'

Here, we approximate the actual shape of the nanowires by a cylinder with radius R, length l, and homogeneous mass density p. The acoustic vibrational modes of an infinite cylinder can be classified into three types: longitudinal modes, torsional modes, and flexural modes [17].

The longitudinal modes represent the vibrations of the atoms around their equilibrium positions, where the displacements of the atoms are mostly parallel to the direction of the nanowire [17]. In contrast to bulk longitudinal modes, there is also a small radial component due to the Poissons ratio. The angular frequency œ of each mode is related to its wavevector k by the following relation:

œ — ek,

this relation is called the dispersion relation and the proportionality constant is the mode velocity. The longitudinal modes velocity Clong have the form

In the torsional vibrations, the radial displacement of the atoms about their equilibrium positions is perpendicular to

the direction of the wave propagation. The torsional modes also have linear dispersion relation as in (5), and the torsional modes velocity ctor has the following form:

The flexural modes are more complicated than the previous modes. The dispersion relation of the flexural modes is quadratic

œ = fflexk2, (8)

where the proportionality factor of the flexural modes reads

ER2 4p

Simulating a finite nanowire by COMSOL, we obtain directly the set of eigenfrequencies. From the spatial structure, see Figure 1, we determine the character of the modes and determine the wavevector k = 2n/X by a close inspection of the spatial periodicity of the mode (with period X) in the wire direction. One can clearly identify the different branches from the infinite wire. Figure 2 shows the calculated lowest frequencies for GaAs nanowire with isotropic approximation of length 225 nm and radius 20 nm. In this way, we obtain the dispersion relations (5), (8). From the data in Figure 2, we extract the velocities Clong = 3890 m/s and ctor = 2484 m/s. These values are very close to the theoretical values given by (6) and (7), clong = 4020 m/s, ctor = 2484 m/s. The extracted proportionality factor of the flexural modes fflex = 4.7 * 10~5 m2/s also agrees roughly with the theoretical value given by (9), fflex = 4 * 10~5 m2/s. We conclude that our procedure allows to obtain reliable data for the dispersion relations.

3. Isotropic Approximation versus Cubic Nanowire

In this section, the isotropic symmetry, which manifests the same result at any direction, will be compared to the actual cubic symmetry of GaAs. As is well known and mentioned above, the cubic symmetry has three distinct elastic moduli whereas the isotropic material has only two independent elastic constants. The question that arises currently is how the dispersion relations of phonon modes, in material with cubic symmetry, will differ from those that have been displayed previously with isotropic symmetry. The COMSOL simulation tool allows for a treatment of both types of symmetries, which are directly compared in this section. For this purpose, we study the phonon modes in GaAs nano-wires along [001] direction. In Figure 3, one can easily notice the difference between the dispersion relations of the two kinds of symmetries. The longitudinal modes have similar dispersion relations in both, and they have almost identical longitudinal velocities in the both symmetries. The dispersion relation of the flexural modes in the two types of symmetries are similar at lower frequencies, but they

Table 1: The density (p) and the elastic properties Young's modulus (E) and Poissons ratio (v) of materials of zincblende structure that considered in this work as isotropic material.

Table 3: The density (p) and the elastic moduli of materials with wurtzite symmetry.

Material P (kg/m3) E (GPa) v Material p (kg/m3) C11 (GPa) C12 (GPa) C13 (GPa) C33 (GPa) C44 (GPa)

GaAsa 5318b 85.9 0.31 GaNa,d 6095b 390 145 106 398 105

AlAsa 3598 83.5 0.32 AlNc,d 3255b 410 148 99 388 130

InAsc InPd

5667b 4810

51.4 61.1

0.35 0.36

Elastic properties are from [ 18]. [17].

Elastic properties are from [19]. [20].

Table 2: The elastic moduli of materials with cubic symmetry.

Material C11 (GPa) C12 (GPa) c44 (GPa)

GaAsa 118.8 53.8 59.4

AlAsa 120.2 57 58.9

a: [21].

manifest a divergence at high frequencies. More noticeable, the torsional modes exhibit a significant difference in their dispersion relations, as shown in Figure 3. For the cubic material, we extract ctor = 3343 m/s, while the isotropic approximation provides ctor = ^/p = 2484 m/s as addressed above. This difference can be elucidated by the fact that the Lame coefficients extracted from the material parameters in Table 1 by (4) satisfy X = ci2 and ^ = (cn - ci2)/2 for the cubic parameters from Table 2. Now, the isotropic approximation, see (3), requires c44 = (c11 -c12)/2, which, however, does not hold exactly for cubic materials; see Table 2. In contrast, the observed velocity ctor for the torsional modes equals .^c44/p in this case. As c44 > (c11 - c12)/2, the isotropic approximation underestimates the torsional velocity in [001] direction.

4. Acoustic Phonons in Nanowire Heterostructure

Now, we consider acoustic phonons in nanowire heterostruc-tures in order to compare the results to those of simpler pure nanowires. We consider structures, where the wires consist of segments of different materials stacked in the wire direction as experimentally realized in [11]. Note that the interfaces between the materials are perpendicular to the wire direction in contrast to the case intensively studied by Balandin and coworkers [22], where the interfaces are parallel to the wire direction. Due to the lacking translational invariance in the wire direction, k is not an exact quantum number for the phonon modes in our case. Nevertheless, we can still extract an average distance X between nodes or maxima in the mode profile as discussed above, and thus obtain an effective k = 2n/X for comparison with the ideal wires.

We consider a nanowire of total length 225 nm. In the middle, there is GaAs region with length 35 nm, embedded between two barriers of AlAs of thickness 5 nm. The outer

Elastic moduli are from [23]. [17].

Elastic moduli are from [24]. [16].

regions are again GaAs. This structure constitutes the prototype of an electron resonant tunneling nanowire device. The acoustic phonons in the AlAs/GaAs/AlAs nanowire hetero-structure display the same behavior as in the pure GaAs nanowire of the same length; see Figure 4(a). Very slight differences in the eigenfrequencies of the phonon modes are observed due to existence of another material, and we checked that these differences are getting larger by increasing the amount of the other material. Consequently, the dispersion relations of all phonon modes are essentially the same in a nanowire and a nanowire heterostructure. For the heterostructure, we extract the values clong = 3898 m/s, ctor = 2494 m/s, and fflex = 4.75 * 10-5m2/s in the iso-tropic approximation, which are slightly larger than the corresponding values for pure GaAs wires are clong(GaAs) = 3881, ctor(GaAs) = 2484m/s, and fflex(GaAs) = 4.7 * 10-5. The main difference can be accounted for by considering an average material of 95.556% GaAs and 4.444% AlAs, corresponding to the composition of the finite wire. Then, we expect


95.556 * Clong(GaAs) + 4.444 * Clong(AlAs)

= 3915 m/s,

and similarly ctor(av) = 2505 m/s and fflex(av) = 4.8 * 10-5 m2/s, which all slightly overestimate the increase.

Similar results have been obtained from the comparison between phonon modes in nanowire and nanowire hetero-structure with the cubic symmetry. The dispersion relations of phonon modes in a cubic pure GaAs nanowire are in full accord with those in a cubic GaAs/AlAs nanowire hetero-structure, as it is illustrated in Figure 4(b). The phonon modes in these two kind of nanostructures have also very small variances in their eigenfrequencies due to the existence of small part of another material which has different elastic properties.

Indium arsenide (InAs) and indium phosphide (InP) also have a zincblende structure with three independent elastic constants. But for simplicity, we have used the isotropic approximation to study the phonon modes in InAs/InP het-erostructure. Then, the dispersion relations of the acoustic phonon modes in InAs/InP heterostructure have been compared to those in a pure InAs nanowire; see Figure 5. It is difficult to distinguish the difference in the frequencies of the modes in a nanowire and a nanowire heterostructure by just looking at Figure 5, due to the smallness of these variances. These small variances arise from usage of different

Figure 1: Examples of the vibrational mode shapes. ( a) Longitudinal mode, ( b) Torsional mode, and ( c) Flexural mode. The vertical axis displays the nanowire height in units if 100 nm.

Wave vector (rad/m)

• - Longitudinal modes ■■»■ Torsional modes ■ ■»■ Flexural modes

Figure 2: Dispersion relations of the acoustic phonons in pure GaAs nanowires with isotropic approximation.

x1011 2.5

fr 1.5 G

M' o' .H .O m ß' > -

a' .■

/"ß" -

/0 ••

Wave vector (rad/m)

Long (isotrop) Long (cubic) Tors (isotrop)

Tors (cubic) Flex (isotrop) Flex (cubic)

Figure 3: Dispersion relations of the acoustic phonons in pure GaAs nanowires with isotropic and cubic symmetries along [001] direction. The results for the longitudinal modes fall on top of each other.

material and it depends on the percentage contribution of each substance in the nanoheterostructure size. We extract the values ciong = 2960 m/s, ctor = 1842 m/s, and _/flex = 3.5 * 10~5 m2/s for the heterostructure wire. Here, the assumption of an average material provides ciong(av) = 2961 m/s, Ctor(av) = 1844 m/s, and /fiex(av) = 3.32 * 10~5m2/s. This approximation works much better for the InAs/InP material system than for the GaAs/AlAs case discussed above (except for the flexural modes, where the coefficient is difficult to extract).

Another way to prove the similarities of the acoustic phonon modes, with small wavevectors, in both pure InAs nanowire and InAs/InP nanoheterostructure are the comparisons of the strain components in both structures. Figure 6 illustrate the likeness of normal strains for the longitudinal modes and the shear strains for the flexural modes in both pure InAs nanowire and InAs/InP nanoheterostructure regardless of the discontinuities of the strain components at the interfaces between InAs and InP segments. One can see mirror reflections around z-axis of some modes in

Long (GaAs) Long (hetero) Tors (GaAs)

Wave vector (rad/m)

о Tors (hetero) ♦ Flex (GaAs) Flex (hetero)

(a) Isotropic approximation

xíg11 2.5

fr 1.5

i2 XiG7

G«1 G

Long (GaAs) Long (hetero) Tors (GaAs)

Wave vector (rad/m)

o- Tors (hetero) ■■♦■■ Flex (GaAs) - О - Flex (hetero)

(b) Cubic symmetry

Figure 4: These figures illustrate that the phonon dispersion relations in pure GaAs nanowire and GaAs/AlAs nanowire-heterostructures are almost identical. (a) GaAs nanowire and GaAs/AlAs nanowire-heterostructure with isotropic approximation. (b) Same structures calculated with cubic symmetry. The wire length is 225 nm in all cases.

Long (InAs) Long (hetero) Tors (InAs)

Wave vector (rad/m)

- о - Tors (hetero) ♦ ■■ Flex (InAs) ■ 0 ■ Flex (hetero)

Figure 5: Dispersion relations of phonons in both InAs nanowire and InAs/InP nanowire heterostructure with the same length 300 nm, which are almost equal to each other.

ture, such as Gallium nitride (GaN) and aluminum nitride (AlN), manifest symmetry in the elastic moduli matrix with five independent constants c11, c12, c13, c33, and c44 [14, 16, 17]; see Table 3. The motivation of studying acoustic phonons in plenty of materials with different structures is to explore whether acoustic phonons might show different behavior in different structures. The dispersion relations of acoustic phonon modes have been drawn in a pure GaN nanowire in Figure 7(a) and a GaN/AlN nanoheterostructure in Figure 7(b). In these structures the longitudinal and torsional modes have linear dispersion relations, as it is observed above for the isotropic and zincblende materials. The flexural modes have two components due to bending of the nanostructure toward (x-axis) and (y-axis). While these are exactly degenerate for cubic materials addressed in preceding sections, these two flexural components become non-degenerate for higher frequencies in the pure GaN nanowire as well as in the GaN/AlN heterostructure. The acoustic phonon eigenfrequencies in the GaN/AlN heterostructure are slightly higher than those in a pure GaN nanowire, and the approximation of an average material again slightly overestimates the trend.

the figures, but with the same strain values. The reason is that the solver in COMSOL multiphysics is solving for the absolute value which may take positive or negative values. Taking this into account, we conclude that the strain profiles are only weakly affected by the presence of the heterostruc-ture.

5. Acoustic Phonons in a Nitride Heterostructure

Another kind of structure has been used in this work, the wurtzite structure. The materials that have wurtzite struc-

6. Conclusion

The phonon dispersion relation, w(k), that holds for an infinite wire, has been extracted from COMSOL calculations in finite nanostructures made of different III-V semiconductors such as GaAs, InAs, and GaN. We find that the dispersion relation of torsional modes has changed significantly during the switching between the isotropic and cubic symmetries, while the longitudinal modes are not influenced at all for a [001] wire direction. For heterostructures, we demonstrated, that the phonon spectrum is only weakly modified and the strain components do not vary essentially. This suggests that

x108 1

X107 1.5

¡5 <u -C

S -0.5

(a) Pure nanowire (longitudinal)

(c) Pure nanowire (flexural)

x108 1

x107 1

(b) Heterostructure (longitudinal)

(d) Heterostructure (flexural)

Figure 6: The normal and shear strains ez and exz of the lowest longitudinal and flexural modes respectively in a cross-section taken in the middle of an InAs nanowire and an InAs/InP nanowire heterostructure with l = 60 nm along z-axis, where the region shown includes two barriers and the quantum well in the heterostructures (calculations in isotropic approximation).

x1011 4

s^ 1 W

Wave vector (rad/m)

Longitudinal modes Torsional modes

■ - 0 ■

Flexural modes-1 Flexural modes-2

(a) GaN nanowire

Wave vector (rad/m)

Longitudinal modes - ■ o ■ ■ Flexural modes-1 Torsional modes -0 Flexural modes-2

(b) GaN/AlN

Figure 7: Dispersion relation ofphonons in a GaN nanowire and a GaN/AlN nanowire heterostructure with the same length 300 nm using the wurtzite symmetry.

one can safely ignore the presence of heterostructures if the lowest phonon branches are needed in calculations for electron scattering processes.


Financial support from the Erasmus Mundus program and the Swedish Research Council (VR) is gratefully acknowledged.


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