Critical issues for homoepitaxial GaN growth by molecular beam epitaxy on hydride vapor-phase epitaxy-grown GaN substrates
Introduction
Gallium nitride-based materials and devices have progressed from the research laboratory to the commercial sector over the past decade, facilitated by improvements in heteroepitaxial growth of group III-N device layers on non-native substrates such as SiC, sapphire, and Si. Heteroepitaxial growth has been necessitated by the limited availability of bulk single-crystal III-N materials that can be used as substrates. However, there have been substantial simultaneous improvements in the growth and availability of bulk nitrides, and a number of groups have already demonstrated a wide variety of devices grown on freestanding GaN substrates, such as light emitting diodes (LEDs) [1], [2], laser diodes [3], [4], [5], [6], [7], [8], [9], solar cells [10], [11], [12], vertical power p–n diodes [13], [14], Schottky diodes [15], and high electron mobility transistors [16], [17], [18], [19], [20], [21], [22], [23], [24], [25], [26], [27].
While high pressure [28], [29] and ammonothermal [30], [31] growth of bulk GaN have resulted in crystals with very low densities of threading dislocations (TDs), i.e.,<102 cm−2 and 5×104 cm−2, respectively, hydride vapor-phase epitaxy (HVPE) has been used most frequently for producing freestanding GaN substrates due to its wider availability, faster growth rates, and larger and more uniform wafer size [32]. The threading dislocation density (TDD) of HVPE-grown GaN substrates is typically 106–107 cm−2, several orders of magnitude greater than for high pressure- or ammonothermally-grown GaN. Nevertheless, the TDD of heteroepitaxial GaN is typically 108–1010 cm−2; hence, homoepitaxy on HVPE-grown GaN offers significant reductions in TDD compared to heteroepitaxy. Thus, a device measuring 10×10 µm2 might reasonably be expected to contain from one to ten TDs on average if fabricated on homoepitaxial GaN layers, but 102 to 104 if fabricated on heteroepitaxial layers.
Section snippets
Development of freestanding HVPE GaN
Naniwae et al. [33] provided one of the first descriptions of GaN grown by HVPE on sapphire, and the subsequent growth of a GaN layer by metal-organic vapor-phase epitaxy (MOVPE). Within two years, Detchprohm et al. [34] reported the growth of high-quality, single-crystal GaN by HVPE on sapphire using ZnO buffer layers. Although they obtained freestanding GaN by etching the ZnO buffer and peeling the films from the substrate, the lateral dimensions were limited to 2–4 mm due to cracking of the
Experiment
We have investigated various methods for preparing Ga-polar HVPE GaN surfaces for homoepitaxial growth. In the following sections we provide details of these methods and describe their effects on microstructure and impurity incorporation in GaN layers grown by plasma-assisted MBE.
Results and discussion
Samples VG2344 and VG2345 were both grown on solvent-only cleaned wafers at a substrate temperature of 650 °C. The only significant difference between the two samples was the insertion of an ultrathin (1.5 nm) AlN NL at the beginning of the layer growth of VG2345. A high density of threading dislocations, primarily edge or mixed dislocations, are visible in XTEM; micrographs of VG2344 are shown in Fig. 4 (the micrographs from VG2345 are very similar and are not shown for brevity). Plan-view TEM (
Conclusions
This paper has reviewed the challenges associated with homoepitaxial GaN growth on freestanding, c-plane HVPE-grown GaN substrates of N- and Ga-polarities, including the chemical reactivity of the surfaces and their susceptibility to thermal decomposition or roughening. Methods are described for preparing these substrates for growth by plasma-assisted MBE in order to obtain homoepitaxial GaN layers with high structural quality and low impurity concentrations. For optimal growth on either the
Acknowledgments
The work at NRL was supported by the Office of Naval Research. The authors also acknowledge the use of the facilities in the John M. Cowley Center for High Resolution Electron Microscopy at Arizona State University.
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Present address: Ames Laboratory, Ames, IA 50011, USA.