Atomistic modeling and HRTEM analysis of misfit dislocations in InN/GaN heterostructures
Highlights
► Identification of misfit dislocations (MD) in-plane configuration in InN/GaN interfaces. ► Energetic mapping designates that MD arrays adopt 〈1 1 −2 0〉 line directions with b = 1/3〈2 −1 −1 0〉. ► Local arrangement of the Moiré fringes depends strongly on the thickness of the TEM foil as revealed by HRTEM image simulations. ► Geometric Phase Analysis on simulated images justifies results obtained by energetic mapping.
Introduction
A milestone in the advancement of III-Nitride-based technology was the identification of the InN band gap value being equal to ∼0.7 eV [1]. Extension of the III-Nitride device operational wavelength range from the deep ultraviolet to the infrared became thus feasible, at least in principle, through alloying of the binary compounds. Laser diodes and photovoltaics based on InGaN and high frequency field effect transistors based on AlInN/GaN heterostructures were recently fabricated while binary InN presents high potential for solar cells as well as chemical and biological sensors (e.g. [2], [3]).
Optimization of III-Nitride devices necessitates identification and thorough understanding of the relaxation mechanisms in employed heterostructures and the atomic arrangement at corresponding interfaces. This need is exemplified in the case of InN/GaN heterostructures since they form a high mismatch system (∼11%) [4] with a critical thickness of ∼2 monolayers [5], which indicates an almost spontaneous generation of misfit dislocations (MDs). Even if low-dimensional systems are exploited in order to enhance carrier confinement and avoid non-radiative recombinations, MDs shall be formed at these interfaces and affect optoelectronic properties (e.g. [6]). Moreover, modeling of interfaces in high misfit heteroepitaxial systems is an elaborate issue, accentuated when the interface comprises more than two MD arrays as in the high symmetry (0 0 0 1) polar interface in wurtzite heterostructures and the proximity of MD lines, in the case of high misfit, becomes so small that MD intersections come very close together.
Following elasticity theory, MDs in (0 0 0 1) III-N heterointerfaces could lie along the or directions. In either case, MDs could intersect in pairs leading to a “Star of David” distribution comprising hexagonal and triangular areas of “good” and “bad” fit respectively, separated by MDs (Fig. 1(a)). Alternatively, the MD lines may intersect in triads forming triple dislocations nodes and exhibiting a hexagonal texture as illustrated in Fig. 1(b).
High resolution transmission electron microscopy (HRTEM) experiments on (0 0 0 1) InN/GaN heterostructures grown by plasma assisted molecular beam epitaxy (PAMBE) revealed that the structural mismatch is effectively accommodated through the formation of a MD network at the interface. This comprises three equally spaced arrays of 60° mixed-type MDs, the projected edge component of which can be resolved as GaN extra half-planes in HRTEM images taken along the axis [4], [7]. The 60° MD network of was evidenced by Kehagias et al. [8] in both compact InN thin films, as well as non-coalesced three dimensional islands grown by PAMBE on (0 0 0 1) GaN/Al2O3 substrates.
Introduction of MDs, with line directions parallel to directions, has been proposed as an efficient scheme for plastic relaxation at the initial stages of InN/GaN growth [9]. A set of three 60° dislocations was also acknowledged as the origin of plastic relaxation in InN QDs in GaN matrix grown by metal-organic vapor phase epitaxy (MOVPE). Hexagonal and triangular areas separated by MDs were observed at the InN/GaN interface, which gave the overall impression of a “Star of David” distribution instead of a hexagonal reconstruction [10]. Interestingly scanning tunneling microscopy (STM) experiments by Liu et al. [11] showed a network of three sets of 90° partial MDs at the InN/GaN (0 0 0 1) heterointerface, which were parallel to but formed a hexagonal network. In contrast to the above, cathodoluminescence experiments at the interface of InGaN/GaN heterostructures grown by MOVPE indicated the formation of a MD network along [12].
Towards resolving the discrepancy of experimental results, atomistic simulations through well established interatomic potentials and the III-species environment approach [13], [14] are essential, since they have proven invaluable in the analysis of structural mechanisms, extended defects and dislocations in III-N semiconductors [15], [16], and can provide the relaxed interface for direct comparison with the HRTEM observations.
In our present study, energetic mapping of the InN/GaN interfacial area, as obtained by atomistic simulations through the III-species environment approach, is performed in order to determine the characteristics of the InN/GaN MD network. Moreover, a detailed analysis of HRTEM simulated images is undertaken, and strain maps along the 〈0 0 0 1〉 direction are obtained in order to establish the local arrangement of Moiré fringes and clarify experimental controversies.
Section snippets
Results and discussion
An efficiently parameterized Tersoff interatomic potential [17] was utilized for atomistic calculations of the InN/GaN interface, considering a plastically-relaxed heterostructure but without prior introduction of a pre-defined dislocation network. Interfacial plane and polarity were taken as variational parameters. Structural models indicating the characteristics of the energetically favorable configurations, namely interfaces of III- or N- polarity cutting single bonds, are illustrated in
Conclusions
In the present study the characteristics of MDs in plastically relaxed InN/GaN interfaces were investigated in order to disambiguate contradictory experimental results. Through a combination of HRTEM observations and image simulations, GPA strain analysis and atomistic calculations, the structural network as well as the line direction and Burgers vector of MDs is elucidated.
Energetic mapping of the interfacial area on the simulated, relaxed InN/GaN supercells elicits that misfit dislocation
Acknowledgement
This work was supported by EC under the 7th European Framework Project DOTSENSE (grant no. STREP 224212).
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