Advances in OptoElectronics

Advances in OptoElectronics / 2011 / Article

Research Article | Open Access

Volume 2011 |Article ID 145012 |

P. J. Carrington, M. de la Mare, K. J. Cheetham, Q. Zhuang, A. Krier, "Midinfrared InAsSbN/InAs Multiquantum Well Light-Emitting Diodes", Advances in OptoElectronics, vol. 2011, Article ID 145012, 8 pages, 2011.

Midinfrared InAsSbN/InAs Multiquantum Well Light-Emitting Diodes

Academic Editor: Yuh-Jen Cheng
Received23 Apr 2011
Revised10 Jun 2011
Accepted05 Jul 2011
Published05 Sep 2011


Electroluminescence is reported from dilute nitride InAsSbN/InAs multiquantum well light-emitting diodes grown using nitrogen plasma source molecular beam epitaxy. The diodes exhibited bright emission in the midinfrared peaking at 3.56 μm at room temperature. Emission occurred from a type I transition from electrons in the InAsSbN to confined heavy and light hole states in the QW. Analysis of the temperature- and current-dependent electroluminescence shows that thermally activated hole leakage and Auger recombination are the performance limiting factors in these devices.

1. Introduction

There is increasing interest in the fabrication of mid-infrared optoelectronic devices for a range of applications including environmental pollution monitoring, remote sensing (LIDAR), infrared counter-measures, and free space optical communications. A number of different semiconductor materials and devices are currently being investigated including InSb/InAs quantum dots [1], bulk GaInAsSbP pentanary [2] and AlInSb alloys [3], InGaAsSb/AlGaInAsSb quantum wells (QWs) [4], and InAs/GaSb superlattices [5]. Recently we reported on bright room temperature electroluminescence from type II InAsSb/InAs multiquantum well (MQW) light-emitting diodes (LEDs) which produced a quasi-cw power of 12 μW corresponding to an internal quantum efficiency of 2.2% at a peak wavelength near 3.7 μm [6]. One way to improve the performance is to introduce nitrogen into the well. The introduction of a small amount of nitrogen reduces the bandgap without excess strain and can change the band alignment from type II to type I increasing the electron confinement and e-h wavefunction overlap. Furthermore dilute nitrides have the potential to reduce Auger recombination [7] and intervalence band absorption.

To date there have been no reports of LEDs based on dilute nitride material in the mid-infrared spectral range (λ > 3 μm) due to the difficulty in growing epitaxial material of sufficient quality. Our previous work has concentrated on the development and optimisation of the growth of InAsSbN and from which photoluminescence (PL) was obtained up to 250 K from InAsSbN/InAs MQWs [8, 9]. It was found that the surfactant effect of Sb enhances the crystalline quality and PL intensity. Also the possibility to adjust the Sb and N contents in the material enables one to grow the material lattice matched to InAs or to tailor the strain in the QW. In this work we report bright room temperature electroluminescence at 3.56 μm from InAsSbN/InAs MQW LEDs and investigate the temperature and current dependencies of the confined transitions in the QWs.

2. Sample Growth and Fabrication

The LED (Figure 1(a)) was grown by solid source molecular beam epitaxy (MBE) on (001) InAs substrates using a radio frequency plasma nitrogen source. Thermal effusion K-cells were used to supply the group III fluxes and two Veeco valved cracker cells were used to provide the antimony and arsenic fluxes. A 0.5 μm n-type InAs(Te) layer was grown first at 490°C at 1 μm/h, followed by the MQW active region which was grown at 410°C, with a growth rate of 0.5 μm/h. The thicknesses of the well and barrier layers were 10 and 25 nm, respectively. An undoped 30 nm Al0.9Ga0.1As0.21Sb0.79 electron blocking barrier was grown 100 nm above the active region and finally a 0.5 μm p-type InAs(Be) layer was grown at 490°C. The QWs were grown using the same shutter sequence as described previously [6] to improve the interface abruptness. For the growth of the QWs the nitrogen plasma setting was fixed at a power of 210 W and a nitrogen flux of 7.0 × 10−7 mbar, whilst the Sb and As fluxes were set at 1.1 × 10−6 and 2.6 × 10−6 mbar, respectively. During the QW growth the RHEED pattern showed a clear 1 × 3 pattern which quickly changed to 2 × 4 under the As2 soak prior to the growth of the barrier. High-resolution double crystal X-ray diffraction (DCXRD) was used to determine the N and Sb compositions. The resulting wafers were then processed into 1 mm diameter mesa-etched LEDs using standard photolithographic techniques and mounted on TO-46 headers. The devices were tested at 1 kHz using a 50% duty cycle and the electroluminescence (EL) was measured using a Bentham 0.3 m monochromator and 77 K InSb photodiode. Output power at room temperature was measured using an integrated sphere and calibrated PbSe photodetector.

3. Results and Discussion

Figure 2 shows the X-ray diffraction spectrum measured from one of the LEDs which shows a number of well-defined satellite peaks, where the FWHM of the satellite peaks is around 80 arcsecs characteristic of a high structural quality. This is slightly higher than previous InAsSb/InAs MQWs [6] indicating that some minor structural disorder has been introduced by the nitrogen. The broader peak around 1000 arcsec is from the AlGaAsSb barrier (which was nonintentionally grown slightly lattice mismatched). Simulation of the XRD curve gives the Sb and N contents in the well as 5.0% and 0.8%, respectively, so that the strain in the QW is approximately 0.2%. The band structure at 4 K for the QW is shown in Figure 1(b) using the same calculation procedure as described previously [9]. Three heavy hole and one light hole states are confined. The transition energies and localization energies are given in the adjacent table. As the e1 localisation energy is negligible ~4 meV, one can ignore the electron confinement in the QW.

The temperature-dependent current-voltage (I-V) curves measured from one of the LEDs are shown in Figure 3. The series resistance was calculated to be ~2.5 Ω and was found to be independent of temperature. The leakage current in narrow gap semiconductors is much more problematic than at shorter wavelengths due to the higher intrinsic carrier concentration and intrinsic point defects [10] and this is reflected in the device I-V characteristics. In this case the diode leakage current was found to be 2 mA at 0.5 V at room temperature which is lower than InAs-based devices made previously in our laboratory [11] and comparable to those reported in [12]. With decreasing temperature the leakage current decreases to 8 × 10−4 A at 0.5 V (at 4 K) and is almost temperature independent over the 4–150 K range suggesting that the process responsible for leakage could be due to tunnelling effects. At low temperatures the occupation of traps is higher meaning that the forward and reverse currents at 0.5 V are similar in magnitude. Reduction in surface states to reduce the leakage current and to improve device performance can be expected using surface passivation as demonstrated previously [13]. At room temperature the zero bias differential resistance area product (R0 A) was determined to be 1.7 Ω·cm2. Analysis of the slope near the origin gives a value of 2 for the ideality factor indicating that generation recombination current dominates.

Low temperature (4 K) electroluminescence (EL) emission spectra measured from the LED at various currents are shown in Figure 4. At 30 mA a single symmetric peak is observed at 0.366 eV with a FWHM of 11 meV. This agrees well with the value of 0.357 eV calculated for the electron-heavy hole (e-hh1) transition (Figure 1(b)). As the current increases there is a small blue shift ~2 meV of the peak position due to band filling and two high energy shoulders appear. The inset of Figure 4 shows the deconvolution of the spectrum at 150 mA into three Gaussian peaks where the peak emission energies are 0.368, 0.384, and 0.415 eV. The latter two peaks correspond to recombination from e-lh1 (calculated value of 0.395 eV) and InAs. The small blue-shift of the QW emission peak (2 meV) compared to type II InAsSb/InAs (~8 meV) [6] suggests that the band alignment is type I. Furthermore, the type II InAsSb/InAs followed a current1/3 behaviour due to band bending at the type II interface whereas no such dependence was found for the InAsSbN/InAs QWs.

The temperature-dependent EL at an injection current of 100 mA is shown in Figure 5. Emission from e-hh1 in the QW is the main peak which is observed up to room temperature whereas, emission from e-lh1 is not observed above 150 K. At high temperatures () a high energy tail is observed due to the Boltzmann thermal distribution of carriers. The temperature dependence of the peak energy is shown in Figure 6.The solid lines represent the fitting results using the empirical Varshni equation [14] where (0), , and are Varshni parameters and is the measured temperature. The values obtained for the Varshni fitting parameters are given in the table along with reference values for InAs and InAsN [15, 16]. The temperature dependence of the InAsN bandgap is much less than that of InAs (lower value of ) and the values for InAsSbN are slightly higher than InAsN. The carrier localization energy at a given temperature is given by [17] where is the experimental PL peak. At 4 K the localization energy is 4 meV which decreases to zero at 80 K. The weak localization energy is related to the good structural quality and improvement in the nitrogen homogeneity produced by the surfactant effect of Sb.

Figure 7(a) shows the temperature quenching for the e-hh1 transition, normalized to 1 at 4 K, where the integrated intensity drops by two orders of magnitude from 4–300 K. Figure 7(b) is an Arrhenius plot of the same data from which an activation energy of 60 meV was obtained from the high temperature region. This energy is attributed to the leakage of holes out of the QW (the energy is close to the calculated hh1 localization energy of 56 meV) and is considered to be the main reason for the quenching of the luminescence. As noted previously the lh1 transition is not observed above 150 K as the localization energy is only 18 meV and holes can easily escape above this temperature.

Figure 8(a) shows the room temperature LED emission spectra measured using different currents where the peak emission occurs at 0.345 eV with a FWHM of 58 meV. (The slight asymmetry on the low energy side of the peak is due to hydrocarbon absorption contamination on the cryostat window.) LED output power (using 1 kHz ac injection current at 50% duty cycle) was measured at room temperature using an integrating sphere and calibrated PbSe photodetector (Figure 8(b)). An output power of approximately 6 μW was obtained at 100 mA corresponding to an internal quantum efficiency of around 1% which is comparable to other devices made previously in our laboratory [1] and in [18]. The inset of Figure 8(b) shows the data on a log-log plot where the gradient yields the value of where is used to identify the dominant recombination mechanism [19]. Depending on whether the value obtained for is closer to 1, 2, or 3, the dominant term is SRH, radiative, or Auger recombination. It can be seen that for currents between 30–100 mA the value of is close to 2 indicating that radiative recombination dominates whereas at currents between 120–300 mA the value of changes to 3 indicating the onset of Auger recombination at high carrier concentrations. We therefore attribute the low output power and the sublinear -characteristics measured from the device due to a combination of Auger recombination and hole leakage, although current crowding may also be a contributing factor at high injection.

Despite the successful growth and demonstration of EL from the InAsSbN QWs, the output power and efficiency at room temperature is lower than type II InAsSb/InAs QW LEDs made previously in our laboratory [6]. This is primarily due to the lower valence band offset (62 meV for InAsSb0.05N0.008/InAs compared to 86 meV for InAsSb0.08/InAs QWs) since less Sb was incorporated into the InAsSbN QWs such that holes can escape more easily. We also note that in the type II InAsSb/InAs QWs the emission is predominantly from the excited hh2 state at room temperature which increases the output power. No EL from the excited hole state is observed in the type I InAsSbN/InAs QWs due to selection rules and the shorter carrier lifetimes. Figure 9 plots the temperature dependence of the normalized integrated intensity for the individual transitions in both samples. It can be seen that in the temperature range 4–180 K the intensity from the e-hh1 transition in the InAsSbN/InAs wells is much higher and more stable than that from the InAsSb/InAs wells due to the larger radiative recombination rate. At higher temperatures the intensity drops dramatically (at a rate comparable to the e-hh1 transition in InAsSb/InAs) due to the loss of holes from the QW. In the InAsSb/InAs QWs, holes can escape from the ground state to the InAs barrier (as no emission is observed from InAs we assume they undergo Auger recombination) or be excited into the hh2 state. Here as observed they can recombine radiatively which improves the temperature quenching and output power of the LED.

To improve the performance of the device it is necessary to increase the hole confinement energy and heavy hole splitting in the wells and to confine electrons by increasing the conduction band offset. The former can be achieved by increasing the Sb content in the well and the latter by increasing the nitrogen content in the well. However, this is not straightforward since both effects work against each other. Increasing the nitrogen content reduces the compressive strain in the quantum well which reduces the valence band offset and the hh1-hh2 splitting. Increasing the Sb content increases the valence band offset but pushes the conduction band upwards which cannot be compensated easily by increasing the nitrogen content. These effects are illustrated in Figure 10 which plots the emission energy and band offsets for given amounts of Sb and N. We estimate that using between 8–10% Sb and 2.5% N in the well will give 82–104 meV hole and 57–65 meV electron confinement with an emission energy 256–270 meV at 4 K. Alternatively, the barrier height could be increased by using a wider band gap material such as InAsSbP or InGaAs(N) which will be the subject of our future work.

4. Conclusion

In summary, InAsSbN/InAs MQW LEDs have been grown by MBE which exhibit excellent structural quality and bright EL up to room temperature. The EL was identified as originating from a type I transition from electrons in the InAsSbN to confined hole states. Analysis of the temperature dependence of the EL suggests that thermally activated hole leakage is a limiting factor in these devices and that Auger recombination dominates at higher currents (I > 120 mA). Further optimization of the QW band structure is anticipated to lead to mid-infrared devices which could be used in a variety of technologically important applications.


The authors would like to thank EPSRC for the award of a studentship to M. de la Mare and K. J. Cheetham. They also wish to thank J. Statter for his skilled technical support.


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Copyright © 2011 P. J. Carrington et al. 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.

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