Effects of Annealing on GaAs/GaAsSbN/GaAs Core-Multi-shell Nanowires
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The effects of ex-situ annealing in a N2 ambient on the properties of GaAs/GaAsSbN/GaAs core-multi-shell nanowires on Si (111) substrate grown by self-catalyzed molecular beam epitaxy (MBE) are reported. As-grown nanowires exhibit band edge emission at ~0.99 eV with a shoulder peak at ~0.85 eV, identified to arise from band tail states. A large red shift of 7 cm−1 and broadened Raman spectra of as-grown nanowires compared to that of non-nitride nanowires confirmed phonon localization at N-induced localized defects. On annealing nanowires to 750 °C, there was no change in the planar defects in the nanowire with respect to the as-grown nanowire; however, vanishing of the photoluminescence (PL) peak corresponding to band tail states along with enhanced band edge PL intensity, recovery of the Raman shift and increase in the Schottky barrier height from 0.1 to 0.4 eV clearly point to the efficient annihilation of point defects in these GaAsSbN nanowires. A significant reduction in the temperature-induced energy shift in the annealed nanowires is attributed to annihilation of band tail states and weak temperature dependence of N-related localized states. The observation of room temperature PL signal in the 1.3 μm region shows that the strategy of adding small amounts of N to GaAsSb is a promising route to realization of efficient nanoscale light emitters with reduced temperature sensitivity in the telecommunication wavelength region.
KeywordsDilute nitrides Nanowires Annealing effects Schottky barrier Point defects
Dilute nitride III–V semiconductor alloys in thin films with variable bandgap have been on the extensively studied material systems [1, 2, 3, 4, 5, 6, 7, 8, 9, 10] for optical telecommunications applications. Introduction of very low nitrogen concentrations is sufficient to modulate the band gap of such systems over a wide range. Amongst the possible III–V-based dilute nitride materials, GaAsSbN systems in the thin film configuration have been proven to be one of the promising systems for the spectral window of 1.3–1.55 μm . Simultaneous reduction in the band gap with lattice parameter and also independent tuning of conduction and valence band offsets by the N and Sb constituents, respectively, are the distinguishing features of this system. However, large disparity in the atomic radius of N and Sb creates N-induced defects and compositional disorder leading to non-radiative recombination centers, which adversely affect the optoelectronic properties of the thin film. It is well established that considerable improvement in the optical properties occurs on annealing due to the annihilation of N-related centers. Reducing dimensionality further to nanowires, for example, may prove to be advantageous for this system in terms of efficient annihilation of point defects and enhanced photon collection due to the large surface to volume ratio.
However, little work has been reported on dilute nitride GaAsSbN nanowires due to the complexities involved in growth of quaternary alloy nanowires. Recently, we have reported successful growth of self-catalyzed GaAs/GaAsSbN/GaAs core-multi-shell nanowires emitting at ~1.3 μm . These nanowires exhibited planar defects in addition to point defects, which is in contrast to thin films where only the latter dominates . Thus, it is necessary to investigate the effect of defects and annealing on dilute nitride nanowires to understand and improve the optical properties.
In this work, we present the effects of ex-situ rapid thermal annealing (RTA) on the optical properties of GaAs/GaAsSbN/GaAs nanowires grown by self-catalyzed molecular beam epitaxy (MBE). Various characterization techniques, namely, transmission electron microscopy (TEM), low temperature μ-photoluminescence (PL), Raman spectroscopy and current (I)-voltage (V) measurements were used to ascertain the nature of defects being annihilated. Temperature dependent PL was examined to understand the effects of localized states and recombination mechanisms.
Nanowire Growth and Characteristic Analyses
The growth of dilute nitride GaAs/GaAsSbN/GaAs core-shell nanowires was carried out on Si (111) substrates by plasma-assisted MBE. GaAs core nanowires were grown at 620 °C with Ga as a catalyst and an As flux with a beam equivalent pressure (BEP) of 4.8 × 10−6 Torr. The growth temperature was then lowered, and GaAsSbN shell growth was initiated at 540 °C by opening the Sb and N shutters. A constant Sb BEP of 1.4 × 10−6 Torr and N BEP of 1.8 × 10−7 were used for the quaternary shell. Both the Sb and N shutters were closed for growth of the final GaAs shell at 540 °C. Detailed growth procedures and characterization techniques are provided in our previous reports [11, 13, 14]. Basically, TEM, PL, and Raman were used to reveal differences in these nanowires before and after annealing. All the nanowires were annealed in N2 ambient using a Jipelec JetFirst 100 RTA for 30 s. For I–V measurements on an ensemble of nanowires, the array of nanowires were initially spun with polymethylmethacrylate (PMMA) which was plasma etched to 200 nm in order to expose the tips of the nanowires. The top contact was Ti (50 nm)/Au (200 nm) while the back contact was Ti (200 nm). To avoid possible short circuits at the sample edges, the top contacts were deposited using a shadow mask consisting of an array of 1-mm-diameter circular apertures to produce discrete contact pads. Then, a contact on the bottom of the substrate was deposited by electron beam evaporation. Electrical measurements were performed at room temperature using a Keithley 4200 characterization system by a two-probe method.
Results and Discussion
Contributors to band tail-induced states include compositional fluctuations, localized defect states, and inhomogeneous lattice deformation . With increasing annealing temperature, the intensity of band to band emission increases by fivefold with a corresponding decrease in the full width at half maxima (FWHM) of the PL peak while the intensity of the N-related defect peak at 0.85 eV gradually diminishes. This latter peak ultimately vanishes for nanowires annealed at 750 °C. These are typical signatures for annihilation of N-related defects, which results from significant reduction in the density of recombination centers responsible for non-radiative processes as in thin films. Suppression of these non-radiative centers facilitates PL emission from higher energy states, which leads to increased PL intensity [8, 9, 16, 18] with increasing annealing temperature. An emission peak at 0.93 eV is also observed in all the samples including unannealed ones. The origin of this peak is not clearly understood; however, it is likely related to compositional fluctuations originating from N incorporation as it merges with the band-band peak for nanowires annealed at 750 °C. In addition, evolution of a distinct PL peak at 1.2 eV at 700 °C which becomes a hump at higher annealing temperature of 750 °C corresponds to a band to band transition of the host non-nitride composition of GaAsSb with 10 at.% of Sb.
In the low-temperature regime, with rising temperature, the excitons confined in the local potential minimum obtain sufficient thermal energy to surmount small barriers and thus relaxing to lower energy states. The recombination of these excitons is responsible for the reduced PL emission energy causing an initial red shift. With further increase in temperature, the excitons gain sufficient energy to populate the higher energy band tail states, and the recombination from these states is responsible for the observed blue shift in the band gap. For temperatures in the region of 75 to 140 K, depending on the sample, corresponding to the highest PL peak energy, the excitons are delocalized. Beyond this temperature, free carrier recombination dominates, and the regular temperature-induced band gap shrinkage occurs due to the electron-phonon interaction and lattice relaxation. Although the overall temperature behavior of the PL in thin films and nanowires is the same, in the nanowires, an additional red-blue shift is observed around 50 K. Such an additional feature is normally reported to be due to splitting of the heavy hole (HH) and light hole (LH) leading to the corresponding excitonic transitions . However, the PL spectra shown in Fig. 2 did not exhibit any distinct peaks that would correspond to LH and HH transitions. X-ray diffraction of the annealed GaAsSbN nanowires (not shown here) exhibited only (111) GaAs peak and did not exhibit any other distinct peak as reported previously  on as-grown nitride core-shell nanowires. This can be considered as evidence of a lattice-matched GaAs/GaAsSbN/GaAs core-shell structure, which suggests that any contribution of a strain component to the splitting of HH and LH is negligible. We, therefore, speculate and assign the additional low-temperature feature to the differences in the electron-phonon interaction with the HH and LH excitons becoming more pronounced for lower dimensional structures  although the energy splitting between HH and LH excitons may be small.
The pronounced S-curve for unannealed nanowires and nanowires annealed at 650 °C suggests a strong localization energy, which is measured to be 31–42 meV. The localization energy reduces to 18.6 and 8 meV with increasing annealing temperature to 700 and 750 °C, respectively, which is indicative of efficient annihilation of band tail states leading to decreased potential fluctuations. This is also further supported by the increase in the PL intensity and narrowing of the full width at half maxima (FWHM) of the PL spectra (Fig. 2). Another dramatic change that is observed with increasing annealing temperature is a reduction in the energy shift between 4 and 300 K, ΔEg (4–300 K), 129 meV for unannealed nanowires to 32.4 meV for the samples annealed at 750 °C as shown in Fig. 3b. These ΔEg values are consistent with our prior work on GaAsSbN quantum wells (QWs) where in situ annealing in an As ambient corresponded to efficient annihilation of N-related centers [9, 16]. In unannealed and at the lower annealing temperature of 650 °C, the localized N level is coupled with extended states of the conduction band [26, 27]. This can be described by a band anti-crossing (BAC) model and exhibits the characteristic temperature-induced band gap shrinkage. In the annealed nanowires where the band states are efficiently annihilated, the temperature-independent characteristic of the N level prevails. A low activation energy for point defects has been cited as the reason for the annihilation of point defects caused by the movement of the lattice atoms on annealing below a critical temperature . Our data are consistent with an optimum annealing temperature in the range of 700–750 °C for effective annihilation of point defects in a thin film configuration [8, 29]. These are very promising results and can have favorable impact in the temperature-induced shift in device characteristics. The room temperature PL of these samples is in the 1.3 μm region (Fig. 3a inset), the wavelength of great interest for photonic integrated circuits.
In conclusion, the effect of ex-situ annealing of GaAs/GaAsSbN/GaAs core-multi-shell nanowires in a N2 ambient has been investigated. With a shoulder at lower energy attributed to band tail states, 4 K μ-PL spectra of the unannealed nanowires display a peak at ~0.99 eV. Raman spectra of as-grown dilute nitride nanowires exhibited a large red shift of 7 cm−1 and were broadened in comparison to that of reference non-nitride nanowires, confirming phonon localization at N-induced localized defects. Rapid thermal annealing of these nanowires in a N2 ambient has been employed to annihilate various N-induced defects. With increase in annealing temperature from 650–750 °C, the PL peak at lower energy corresponding to band tail states vanishes and also the Raman spectra revert back towards the reference spectra, which are considered as clear evidences of annihilation of N-related defects. Significant increase in the Schottky barrier height of the nanowires annealed at elevated temperature also provided further support to the above inference. The temperature-dependent PL spectra exhibited the well-known S-curve behavior, a characteristic of dilute nitride material systems and a signature of exciton localization. Further, room temperature emission and suppression of the temperature-induced band gap in the annealed nanowires are the added attractive attributes offered by these dilute nitride nanowires towards nanoscale optoelectronic device applications.
This work is supported by the Army Research Office (W911NF-15-1-0160, technical monitor-William Clark). The authors acknowledge the use of the Analytical Instrumentation Facility (AIF) at North Carolina State University, which is supported by the State of North Carolina and the National Science Foundation.
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