Well-crystallizedβ-SiC nanorods grown on electrospun nanofibers were synthesized by carbothermal reduction of Tb doped SiO2(SiO2:Tb) nanofibers at 1,250 °C. The as-synthesized SiC nanorods were 100–300 nm in diameter and 2–3 μm in length. Scanning electron microscopy (SEM) results suggested that the growth of the SiC nanorods should be governed by vapor-liquid-solid (VLS) mechanism with Tb metal as catalyst. Tb(NO3)3particles on the surface of the electrospun nanofibers were decomposed at 500 °C and later reduced to the formation of Tb nanoclusters at 1,200 °C, and finally the formation of a Si–C–Tb ally droplet will stimulate the VLS growth at 1,250 °C. Microstructure of the nanorod was further investigated by transmission electron microscopy (TEM). It was found that SiC <111> is the preferred initial growth direction. The liquid droplet was identified to be Si86Tb14, which acted as effective catalyst. Strong green emissions were observed from the SiC nanorod samples. Four characteristic photoluminescence (PL) peaks of Tb ions were also identified.
KeywordsSiC nanorods Vapor-liquid-solid mechanism Terbium Electrospinning Photoluminescence
SiC nanomaterials have promising applications in electronics and photonics owing to their attractive optical, electrical, mechanical, and thermal properties . In particular, SiC nanorods have excellent mechanical and field emission properties, which find potential applications in various nanocomposite materials and in field emission nanoscale devices [2–4].
Since the first synthesis of carbide nanorods using carbon nanotube as templates by Dai group , SiC nanorods have been successfully synthesized by various methods. Vapor-liquid-solid (VLS) growth mechanism is one of the methods that have been extensively employed [6–10]. VLS mechanism was first developed by Wagner and Ellis for the growth of silicon whiskers . The primary feature of VLS mechanism is that the liquid metal alloy droplets sit on the tip of the nanorods and act as the catalyst for the continued growth of the nanorods. For SiC nanorods, Fe, Co, Ni, and Al metals are the most common catalysts used in the VLS process [3, 4, 6, 8–10]. Most of these metals used as catalyst can stimulate only the growth of the nanostructures, but not affect the properties of the samples. Recently, rare earth Tb was used as a catalyst for the growth of GaN nanowires .
In this study, SiC nanorods were synthesized through the conventional carbothermal reduction of electrospun SiO2:Tb nanofibers. The as-grown SiC nanorods possess unique morphologies and show good properties. It is concluded that Tb is a good catalyst for the growth of SiC nanorods. Growth mechanism and PL properties of the Tb doped SiC nanorods were mainly discussed.
First, SiO2:Tb nanofibers were prepared by electrospinning technique . 1 ml of tetraethyl orthosilicate (SiO2 ≥ 28%), 3 ml of ethanol (≥99.7%), 0.5 g of polyvinyl pyrolidone (PVP) (Sigma–Aldrich, M w ≈ 1,300,000), 0.03 g of Tb(NO3)3 · 6H2O, 0.5 ml of acetic acid, and 0.5 ml of N N-dimethyl formamide (DMF) were dissolved together into one mixture. This work was performed under a strong magnetic stirring. After stirred for 2 h, the mixture was sent to an improved electrospinning setup, which was equipped with a heating capability. Then a voltage of 12 kV and a distance of 21 cm were set to the experimental setup. After spinning, SiO2:Tb nanofibers were collected on a clean silicon wafer in the air. Finally, the as-spun samples were pretreated at 1,200 °C in a close round alumina crucible with a graphite inwall, i.e., a carbothermal environment, for 1 h, and then annealed at 1,250 °C for another hour.
The as-synthesized samples were characterized and studied by X-ray diffraction (XRD, Philips, X’pert Pro, Cu Kα, 0.154056 nm.), field-emission scanning electron microscopy (FE-SEM, Hitachi S-4800), and transmission electron microscopy (TEM, JEOL JEM-2010), equipped with selected area electron diffraction (SAED) and energy dispersive spectroscopy (EDS). The micro-PL and micro-Raman spectra of the samples were obtained by using a micro-Raman spectroscopy (JY-HR800, 325 nm exciting source of a He–Cd laser).
Results and Discussion
To investigate the initial stages of VLS growth in this case, the annealing time at 1,250 °C was set to 5 min, and then TEM was used to reveal the microstructure of the nanorods. Figure 4a is a low-magnification TEM image of a nanorod grown on a nanofiber. The nanorod can be divided into two sections, which indicate two different growth directions of the SiC nanorod. This is similar to the top parts of many nanorods presented in Fig. 3c.
As shown in Fig. 4b and c, SAED patterns indicate that the stem of the nanorod should be well-crystallizedβ-SiC grown along the <111> direction, which is consistent with the XRD pattern shown in Fig. 1a. The tip of the nanorod should consist of a mixture of Si–Tb compositions, which may attribute to the large Raman shift of LO modes ofβ-SiC shown in Fig. 1b. The brightest diffraction spot in Fig. 4b corresponds to the SiC <111> direction, while the diffraction ring made up of many small spots may be caused by SiTbxcompounds in the tip of SiC nanorod. Based on the ED spots, the lattice constants can be calculated as 0.3885 and 0.4121 nm, respectively, which are smaller than that of SiC or Si. Referred to the lattice constants 0.3739 nm of TbFe2SiC (JCPDS, No. 47-1093) and 0.4036 nm of Si2Tb (JCPDS, No. 13-0383), it can be suggested that the terbium atoms have penetrated into the SiC lattice, and the end-tip of the nanorod consists of Si–Tb compounds.
High-magnification TEM images of the SiC nanorods (as shown in Fig. 4d and e) indicate that SiC <111> is the preferred growth direction at the initial stage of the VLS growth of SiC nanorods . After the initial growth, if temperature is changed around the growth front of the nanorod, a different growth direction may be selected, and the growth orientation may switch to another SiC <111>, such as . This is similar to the VLS growth of silicon whiskers . In our experiments, once the annealing was terminated, the VLS growth could not stop immediately, and the actual growth condition for the VLS mechanism was changed that resulting in a change of the growth direction and the formation of stacking faults in the samples. This is why most of SiC nanorods shown in Fig. 3c are wry-necked.
Figure 4f and g are EDS spectra collected from the marked areas in Fig. 4a. It can be observed that, leaving out account of Cu from copper TEM grid, the atomic components of the stem and the end-tip of SiC nanorod are Si52.88C22.60O20.72Tb3.80and Si62.82O26.93Tb10.25, respectively. These results suggest that the Tb atoms should be homogeneously doped into the SiC nanorods, which is consistent with our analysis of the SAED patterns.
So far, the emission mechanism of rare earth doped SiC materials is still unclear. Moreover, the most investigated rare earth doping into SiC materials has been focused on erbium (Er). Markmann and Uekusa groups have found that the oxygen impurities can enhance the PL intensity of Er doped SiC materials [21, 22]. Moreover, Gallis group found that the PL intensity of Er doped SiC material depends on the carbon and oxygen content . The strongest PL was observed from the a-SiC0.53O0.99: Er samples, which are quite similar to our samples Si52.88C22.60 O20.72Tb3.80. As to rare earth Tb doping, Xu group have suggested that the oxygen-deficiency centers (ODCs) should contribute to the PL of the doped SiC material . Therefore, combining the previous research, it can be suggested that the Si–C–O compositions have great influence on the enhancement of the green light emission from SiCxOy:Tb nanorods. Furthermore, the unique structure and the quantum confinement effect coming from the nanostructures may also contribute to the PL enhancement of the samples [3, 4].
In summary, well-crystallizedβ-SiC nanorods grown on the SiC nanofibers were synthesized through a VLS process with Tb as the catalyst. The nanorods prepared under a particular process are most straight and long, up to 2–3 μm, with a diameter ranging from 100 to 300 nm. SiC <111> is the preferred growth direction at the initial stage. Once the growth conditions change, the next growth will change to another <111> direction. The effective catalyst in our experiments is Si86Tb14. The EDS and PL results showed that the Tb atoms have diffused into the SiC matrix, and a high-concentration of oxygen impurities in the samples have enhanced the green light emission of SiCxOy:Tb nanorods. The unique structure of the samples and the dopant of rare earth greatly enhanced the PL of the SiC material. This indicates that the rare earth dopant will make the SiC nanostructures good candidates for more photoelectric applications.
This work was financially supported by the Program for New Century Excellent Talents in University of China (Grant No: NCET-04-0975), and partially by the Natural Science Foundation of Gansu Province in China (Grant No: 0710RJZA041). In addition, the authors thank Dr. H.-P. Sun from University of Michigan for helpful suggestion of the manuscript.