Various Quantum- and Nano-Structures by III–V Droplet Epitaxy on GaAs Substrates
- First Online:
- Cite this article as:
- Lee, J.H., Wang, Z.M., Kim, E.S. et al. Nanoscale Res Lett (2010) 5: 308. doi:10.1007/s11671-009-9481-9
- 2.3k Downloads
We report on various self-assembled In(Ga)As nanostructures by droplet epitaxy on GaAs substrates using molecular beam epitaxy. Depending on the growth condition and index of surfaces, various nanostructures can be fabricated: quantum dots (QDs), ring-like and holed-triangular nanostructures. At near room temperatures, by limiting surface diffusion of adatoms, the size of In droplets suitable for quantum confinement can be fabricated and thus InAs QDs are demonstrated on GaAs (100) surface. On the other hand, at relatively higher substrate temperatures, by enhancing the surface migrations of In adatoms, super lower density of InGaAs ring-shaped nanostructures can be fabricated on GaAs (100). Under an identical growth condition, holed-triangular InGaAs nanostructures can be fabricated on GaAs type-A surfaces, while ring-shaped nanostructures are formed on GaAs (100). The formation mechanism of various nanostructures can be understood in terms of intermixing, surface diffusion, and surface reconstruction.
KeywordsDroplet epitaxy Nanostructures High-index GaAs Atomic force microscope Molecular beam epitaxy
Owing to their unique optoelectronic, and physical properties, self-assembled semiconductor quantum- and nano-structures have been the focus of rigorous research efforts in basic physics [1, 2, 3, 4, 5] and solid-state devices. As an example, a number of device applications have been demonstrated, i.e., lasers, detectors, sensors, photovoltaic cells, light-emitting diodes, and solid-state quantum computation [6, 7, 8, 9, 10, 11, 12, 13, 14]. Among diverse self-assembly approaches droplet epitaxy (DE) offers advantages over the conventional Stransky–Krastnov (S–K) approach and thus a unique route to the fabrication of unforeseen nanostructures [15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, 30, 31, 32]. For instance, the lattice mismatch required in S–K approach is not essential in DE approach. In S–K, the lattice mismatch between hetero-systems induces the strain, which has to relax at a critical thickness depending on the amount of mismatch, which leads to the formation of three dimensional (3-D) self-assembled nanostructures . Thus, S–K approach has been widely utilized with such material systems as InAs/GaAs, InP/GaP, and InSb/GaSb. However, in the case of material systems of small or no-lattice mismatch such as GaAs/AlAs or GaSb/AlSb, S–K cannot be adapted to fabricate 3-D nanostructures. In these cases, DE can be utilized to overcome the limitation [16, 28, 29]. Also because of the nature of the S–K growth mechanism, the position of nanostructures in S–K approach is randomly distributed and thus the control is somewhat limited when one solely relies on the S–K. In addition, DE offers higher degree of freedom in the control of size and density of nanostructures. Because the conversion process of liquid-phase metal particles into semiconductors, which is generally referred to “crystallization” or “arsenization,” is not limited to the innate strain or the material system, there is much higher degree of freedom in the control of the size of nanostructures [15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, 30, 31, 32]. Also in DE of certain cases, the metal particle formation and crystallization can be repeated and thus the density of nanostructures can be easily controlled in principle. On the other extreme hand, the optical study of nanostructures requires the fabrication of super low density of nanostructures or subsequent out-situ processes to focus on a singular nanostructure. DE approach can provide ultra low density of nanostructures to the degree of 105 or 106 cm−2, which are several orders of magnitude lower density as compared to that of the conventional method. Furthermore, DE also can be used to fabricate unforeseen nanostructures owing to the flexibility of liquid-phase metal droplets, i.e., unique nanostructures such as quantum dot molecules and ensembles, transition between single and double quantum rings, low-density QDs, and nano-scale templates have been demonstrated [15, 16, 17, 18, 19, 20, 21, 22, 23, 24, 25, 26, 27, 28, 29, 30, 31, 32].
In this article, we show various self-assembled nanostructures by DE approach on various indexes of GaAs surfaces using solid-source molecular beam epitaxy (MBE). Specifically, depending on the DE environment and the choice of index of surfaces, the resulting nanostructures range from InAs QDs and InGaAs ring-shaped nanostructures on GaAs (100) and InGaAs triangular-holed nanostructures on type-A GaAs surfaces. In droplets with the size range suitable for quantum confinement can be fabricated by limiting surface diffusion of adatoms at near room temperatures. Thus, using these droplets, InAs QDs are demonstrated on GaAs (100). Meanwhile super lower density of InGaAs ring-shaped nanostructures can be fabricated on the same index by enhancing the adatoms surface diffusion at comparatively higher temperatures. At a similar growth environment, depending on the choice of index of surfaces, triangular-holed InGaAs nanostructures can be fabricated on GaAs type-A surfaces. The size and density of nanostructures are discussed as a function of substrate temperature and of surface index. Empirical growth models that describe the fabrication mechanisms of various nanostructures by DE are suggested in comparison with the growth condition and indexes of surfaces. This study aids in understanding the formation of various nanostructures on GaAs surfaces by DE approach.
In these experiments, various nanostructures were fabricated on GaAs substrates including (100) and type-A high indexes using solid-source molecular beam epitaxy (MBE). On a molybdenum sample holder, samples were side-by-side mounted using In soldering. Before introducing the samples into a growth chamber, they were pre-treated in a divided degas chamber at 350°C for an hour, which minimized water molecules and other contaminants. In order to calibrate the growth rates of molecular sources and monitor surface reconstructions, an in situ Reflection High Energy Electron Diffraction (RHEED) system was utilized. Native surface Ga oxide was thermally removed at 580°C for 10 min and subsequently a 1-μm thick GaAs homo-epitaxial buffer layer was laid down. The growth rate (Grate) of GaAs was 0.85 monolayer per second (ML/s) under the As4 flux of 6.4 μTorr at 600°C. With an in situ annealing of 10 min to equilibrate the surface matrix, the surface was ready for the further epitaxial growth. As the first step of In DE, the substrate temperature (Tsub) was modified to appropriate ones and the choice of Tsub was mainly dependent on the size and density requirements. For instance, to realize smaller size that is sufficient for quantum confinement and high density enough for applications, the Tsub for the samples in Fig. 2 was chosen to be in the range of 20–35°C. In order to realize the very low density,Tsub was selected to be 250, 350, and 450°C for the results in Fig. 3. In the meantime, for the samples in Fig. 4, the Tsub was fixed at 350°C and the index of the surface was varied to introduce the misfit into the formation of nanostructures. Regardless of the size and density, to prevent background As effects, droplets were formed by applying molecular beams of In under the chamber background below 3 × 10−9 Torr. Droplets form because the bonding energy of In adatoms is greater than that between adatoms and the surface atoms, which is based on the Volmer–Weber growth model . For the samples in Fig. 2, a total amount of 3 ML was deposited on GaAs (100) at a Grate of 0.08 ML/s. Similarly, for the samples in Fig. 3, a total amount of 1 ML was applied at a Grate of 0.08 ML/s on GaAs (100) at corresponding substrate temperatures. For the samples in Fig. 4, the total amount of In deposition was fixed at 1 ML on the entire index of surfaces used and the Grate was 0.05 ML/s. For the fabrication of nanostructures, In droplets were further treated with various fabrication processes depending on the type of nanostructures, which is generally referred to “crystallization” as liquid-phase metal droplets are converted to semiconductors. Generally, crystallization was immediately executed right after the formation of droplets to prevent Ostwald-ripening of droplets [34, 35] and samples were immediately taken out of the chamber after growth processes. Detailed crystallization procedures are discussed in “Results and discussion.” Ex situ atomic force microscope (AFM) characterization was performed in air using tapping mode. The construction of 2D and 3D topographic images and the analysis of data was performed using WSxM software by processing original AFM data .
Results and Discussion
The fabrication of various In(Ga)As nanostructures was demonstrated on various GaAs surfaces by droplet epitaxy using solid-source molecular beam epitaxy (MBE). At near room temperature, with the limitation of surface diffusion of adatoms, InAs QDs were demonstrated on GaAs (100). At higher surface temperatures, because of the enhanced surface diffusion, several orders of magnitude lower density of InGaAs nanostructures were demonstrated at the same surface. While ring-shaped GaAs nanostructures were formed on GaAs (100), triangular-holed InGaAs nanostructures were formed on GaAs type-A surfaces and the density and size was controlled by the selection of the surface index. The growth mechanisms of nanostructures were explained as follows: simple crystallization of In droplets into InAs nano-crystals in the case of QDs. For the ring-shaped and triangular-holed InGaAs nanostructures, the growths were the concurrent result of intermixing, dissolution of GaAs by In droplets and strong anisotropic surface diffusion guided by reconstructed surface matrix. This result can find applications in the formation of quantum- and/or nano-structures based on droplet epitaxy.
The authors acknowledge the financial support of the NSF through Grant No. DMR-0520550 and the ONR through Grant No. N00014-00-1-0506. This research was partially supported by the MKE, Korea under the ITRC Support program supervised by the IITA (IITA-2009-C1090-0902-0018).