InAs/GaAs quantum dots with wide-range tunable densities by simply varying V/III ratio using metal-organic chemical vapor deposition
© Li et al.; licensee Springer. 2013
Received: 21 July 2013
Accepted: 17 August 2013
Published: 28 August 2013
The complicated behaviors of InAs/GaAs quantum dots with increasing V/III ratio associated with several competing mechanisms have been described. The results demonstrate that the densities of InAs quantum dots can be tuned in a wide range from 105 to 1010 cm−2 by simply manipulating V/III ratio via metal-organic chemical vapor deposition. These results are mainly ascribed to the changes of coverage and In adatom migration length due to the increasing V/III ratio.
KeywordsInAs quantum dots V/III ratio MOCVD
Self-assembled InAs/GaAs quantum dots (QDs) have been widely investigated due to their applications in a variety of optoelectronic devices. High-density QD-based structures are usually needed for devices like lasers and solar cells [1–5], while low-density QD-based structures are preferred for devices such as single-photon sources . Due to the great effects of growth kinetics on QDs’ density and size, both high- and low-density QDs may be acquired by choosing suitable growth techniques and carefully tuning growth conditions. In fact, high-density QDs can be acquired quite easily by the Stranski-Krastanov (S-K) growth mode despite of random QDs’ nucleation and size distribution [7, 8]. However, low-density QDs are relatively harder to acquire. Still several approaches have been developed to obtain low-density QDs structures by extremely low growth rate or precise control of the coverage close to the onset of two-dimensional (2D) to three-dimensional (3D) transition [9, 10]. Additionally, some novel approaches such as modified droplet epitaxy [11, 12] and pre-patterning by electron beam lithography combined with etching techniques [13, 14] are also used to grow low-density QDs. Nevertheless, the growth conditions for low-density QDs structures are accordingly very different from those for high-density QDs structures. In this letter, we describe a growth method which demonstrates that the densities of InAs QDs on GaAs(001) substrates can be tuned in a wide range from 105 to 1010 cm−2 by simply manipulating the V/III ratio via metal-organic chemical vapor deposition (MOCVD). This study provides a promising way to achieve reproducible and controllable growth of different QDs-based device structures by MOCVD.
InAs QDs were grown on n-type GaAs(001) substrate via S-K growth mode by Thomas Swan/Aixtron low pressure MOCVD system (Aixtron SE, Herzogenrath, Germany). Trimethylindium (TMIn), trimethylgallium (TMGa), and arsine (AsH3) were used as the source materials with a carrier gas of H2. Prior to the InAs deposition, the substrate was heated to 750°C to remove the native oxides, and then a 500 nm thick GaAs buffer layer was grown at 620°C with V/III ratio of 50. Subsequently, the substrate temperature was lowered to 514°C for InAs QDs growth for 3.5 s. For all the samples studied, the only varied growth parameter was the flux of AsH3 flow. The flow rate of TMIn was fixed at 2.9 × 10−4 μmol·min−1, and the flow rates of AsH3 were varied from 0 to 0.29 μmol·min−1, which means that the V/III ratio was tuned from 0 to 1,000. During growth, the chamber pressure was kept at 150 mBar. After the deposition of the InAs QDs, the growth was interrupted for 30 s and then the substrate was cooled down to room temperature. The QD densities and morphologies were characterized by atomic force microscopy (AFM). For selected samples, 60 nm thick GaAs cap layers were deposited for the photoluminescence (PL) study.
Results and discussion
We describe the detailed behavior of QDs with increasing V/III ratio by three phases as follows:
Phase I. Small increments of AsH3 partial pressure by increasing V/III ratio to 35, 37, 40, and 50 result in rapid increases of well-developed QDs. The QD density increases nearly by five orders of magnitude, from 5 × 105 cm−2 (V/III ratio = 30) to 1.2 × 1010 cm−2 (V/III ratio = 50). Also, the base diameters decrease correspondingly from 90 to 46 nm.
Phase II. By further increasing the V/III ratio from 50 to 140, the densities of QDs increase slowly from 1.2 × 1010 cm−2 to 3.8 × 1010 cm−2, and the corresponding base diameters decrease from 46 to 29 nm. Also, we notice that the uniformity of QDs gets worse and the bimodal size distribution of QDs gets more obvious with increasing V/III ratio.
Phase III. The density of QDs decreases significantly by one order of magnitude when the V/III ratio is increased up to 200, and then increases slowly again with higher V/III ratio. During this phase, the average base diameters also undergo abrupt change, increasing to 121 nm and then decreasing to 90 nm.
To explain the above complicated behaviors of QDs, several competing mechanisms should be taken into account. Phase I is in the margin of 2D to 3D transition which is reasonable to conclude from the AFM images; therefore, a minor increase of coverage can facilitate the growth changing from 2D to 3D, thus resulting in significant change of QDs. As the AsH3 partial pressure increases, the rate of the chemical reaction of TMIn+AsH3→InAs+3CH4 is increased by providing more available AsH3 molecules, leading to the increasing coverage of InAs. As a result, the QD density increases dramatically. A similar behavior of increasing dot density with increasing coverage can be found in many other reports [9, 15, 16]. Meanwhile, the increased AsH3 partial pressure can limit the migration length of In adatoms; therefore, the base diameter tends to decrease. Accordingly, in phase I, with the increasing of V/III ratio, the QD densities increase dramatically and the corresponding QD average diameters decrease.
In phase II, the chemical reaction rate as well as the InAs coverage keeps increasing due to the increasing AsH3 partial pressure, but the increase of the growth rate is limited by the fixed TMIn flow rate. Furthermore, phase II is beyond the 2D to 3D transition; therefore, the QD density increases with decreasing rate. Similarly, the average base diameters decrease due to the limited In migration length with increasing AsH3 partial pressure. In addition, considering the kinetics of MOCVD growth, the initial formation of QDs is not in the thermal equilibrium; thus, increasing coverage also leads to the development of small QDs into energetically favorable large-sized QDs. In our case, the bimodal size distribution starts occurring at V/III ratio of 50 and gets more obvious with increasing V/III ratio.
In phase III, the QD density decreases significantly at V/III ratio of 200. Apparently, a different mechanism may play a dominant role. At high V/III ratio, the available AsH3 molecules are far more than enough for group III species, thus the excess AsH3 may act as impurity-free ‘morphactants’ and raise the surface energy , leading to the suppression of QD formation. This effect becomes prominent with the increase of V/III ratio, finally causing the sudden decrease of QD density at V/III ratio of 200 (phase III). However, with further increase of V/III ratio, the QD density increases gently. The reasons are still not clear at this moment, but in this case, the partial pressure of group III species becomes so low that the possibility of surface reconstruction, which is not detectable during MOCVD growth, may need to be considered. Further experimental works will be conducted to clarify this phenomenon.
In conclusion, we have described the effects of the V/III ratio on the density and sizes of InAs QDs. Due to the effects of several competing mechanisms resulting from increasing AsH3 partial pressure on coverage, In adatom migration length and surface energy, which are the complicated behaviors of QD formation, are observed. The results also demonstrate that the densities of InAs QDs can be manipulated easily in a wide range from 105 to 1010 cm−2 by varying the V/III ratio. Although the initial PL studies show that the optical performance of InAs QDs should be further improved, this V/III ratio-dependent InAs QDs growth approach may prove very useful for the MOCVD growth of different QDs-based device structures due to its simplicity and reproducibility.
LSL, YLL, and JPZ are PhD students at Huazhong University of Science and Technology. QQC and SCS are Master’s degree students at Huazhong University of Science and Technology. JBH and CQC hold professor positions at Huazhong University of Science and Technology. YYF holds an associate professor position at Huazhong University of Science and Technology. QZZ is a PhD student at Sun Yat-Sen University. JTL and XHW hold professor positions at Sun Yat-Sen University.
Atomic force microscopy
Metal-organic chemical vapor deposition
This work was supported by the National Basic Research Program of China (973 Program 2010CB923204), the National Natural Science Foundation of China (grants61006046 and 51002058). We would like to thank Wei Xu, the engineer of WNLO, for the assistance during MOCVD epitaxial growth, and the Center of Micro-Fabrication and Characterization (CMFC) of WNLO for the assistance with the AFM measurement.
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