Phys Rev B 2008, 78:193310.CrossRef Competing AZD5363 purchase interests The author declares that he has no competing interests.”
“Background GaNP has recently attracted much attention as a promising material for applications in optoelectronic and photonic devices, such as light-emitting diodes [1–3]. The incorporation of N click here in GaP allows one to tune the band gap energy and also to change the band gap character from an indirect one in GaP to a direct-like one in the GaNP alloys, leading to improvements in light emission efficiency [2, 3]. A small lattice mismatch of GaNP to Si also provides a unique opportunity to combine high optical efficiency of the III-V compound semiconductors with the capabilities of mature silicon technologies

[4–6]. Unfortunately, the properties desired for optoelectronic applications have not been fully utilized due to the degradation of optical quality of GaNP caused by the

formation of defects that act as centers of non-radiative recombination (NRR) [7]. The NRR processes often dominate carrier recombination and are largely responsible for a reduced optical efficiency of optoelectronic devices [8]. The growth of semiconductor materials in the form of nanostructures, such as nanowires (NWs), often allows suppression of defect formation and therefore offers a possibility to GSK872 overcome the limitation imposed by NRR that is inherent to higher dimensional layers/structures. It also provides increased flexibility in structural design, thanks to confinement effects. In fact

III-V NWs are currently considered as being among the key material systems for future optoelectronic and photonic devices integrated Thymidylate synthase with Si [9–11]. Recently, the epitaxial growth of GaP/GaNP core/shell NWs on Si (111) has been reported [12]. High optical quality of these structures has been demonstrated based on the observation of intense photoluminescence (PL) emission from a single NW [13]. In spite of the high optical quality, fast PL decay caused by NRR processes in the NWs has been reported. The purpose of this work is to gain a better understanding on the quenching processes of the PL intensity from GaP/GaNP core/shell NWs based on temperature-dependent studies by continuous wave (cw) and also time-resolved PL spectroscopies. Methods The GaP and GaP/GaNP NW samples were grown by gas source molecular beam epitaxy (MBE) on (111)-oriented Si substrates [12]. Scanning electron microscopy (SEM) showed that NWs are hexagonal in shape (inset in Figure  1), indicating that NWs were epitaxially grown following the Si [111] crystal orientation. The NWs are uniform in sizes and have an axial length of about 2.5 μm, a total diameter of about 220 nm for the GaP/GaNP NWs, and a typical diameter of approximately 110 nm for the GaP NWs. The N content in the GaNP NW shell was estimated [12] to be approximately 0.9% on average from room-temperature (RT) PL data. For a comparison, a 750-nm-thick GaN0.009P0.