Bi-Assisted CdTe/CdS Hierarchical Nanostructure Growth for Photoconductive Applications
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- Heo, K., Lee, H., Jian, J. et al. Nanoscale Res Lett (2015) 10: 331. doi:10.1186/s11671-015-1037-6
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We developed a method to control the structure of CdTe nanowires by adopting Bi-mixed CdTe powder source to a catalyst-assisted chemical vapor deposition, which allowed us to fabricate CdTe/CdS hierarchical nanostructures. We demonstrated that diverse nanostructures can be grown depending on the combination of the Bi powder and film catalysts. As a proof of concepts, we grew CdTe/CdS branched nanowires for the fabrication of photodetectors. The hierarchical nanostructure-based photodetectors showed an improved photoresponsivity compared to the single CdTe nanowire (NW)-based photodetector. Our strategy can be a simple but powerful method for the development of advanced optoelectronic devices and other practical applications.
KeywordsNanowires Hierarchical structures Photodetector Chemical vapor deposition
Recently, low-dimensional nanostructures of cadmium chalcogenide (CdS, CdSe, or CdTe) have attracted much attention because of their remarkable electronic and photonic properties [1, 2, 3, 4, 5, 6, 7]. In particular, nanowires (NWs) based on cadmium chalcogenide have been considered as versatile building blocks for high-performance optoelectronic devices such as optical waveguides , electrical injection lasers , photodetectors [10, 11, 12, 13, 14, 15, 16], and solar cells [17, 18]. In such optoelectronic devices, a control over the size and the structure of NWs enables the tuning of their energy band gaps and optical properties . Therefore, a lot of studies have been devoted to controlling the structural parameters and morphology of NWs [19, 20, 21, 22]. Especially, many researchers fabricated one-dimensional II-VI heterojunctions to develop high-performance photodetectors [23, 24, 25, 26]. However, the precise control of the NWs with complex hierarchical nanostructures is still a challenge.
Herein, we report a simple, but versatile, method to control the structure of CdTe NWs by adopting Bi-mixed CdTe powder source to a catalyst-assisted chemical vapor deposition (CVD), resulting in NW-based hierarchical nanostructures with largely enhanced photoconductivity. Using our method, we could build well-defined hierarchical nanostructures such as branched NWs or NWs directly grown on cadmium chalcogenide thin films. As a proof of concepts, we fabricated a photodetector based on CdTe/CdS hierarchical nanostructures which showed much larger photoconductivity than photodetectors based only on CdTe NWs. This result shows that our strategy is a powerful way to develop advanced optoelectronic devices with diverse practical applications.
Bi-Assisted CdTe NW Growth
The NWs were grown in a horizontal tube furnace via a vapor-liquid-solid (VLS) process. CdTe powder (Sigma-Aldrich, purity 99.99 %, size < 250 μm) was mixed with Bi powder (Sigma-Aldrich, purity 99.999 %, ~100 mesh) in a 10:1 weight ratio. The mixed powder was placed at the center of an alumina tube furnace as a source material, while an 8-nm-thick Au or Bi film-coated SiO2 substrate was placed at the downstream position of the source material. For the growth of the CdTe NWs, the furnace tube was rapidly heated up to a target temperature of 460~540 °C at a rate of 32.5 °C/min under a constant Ar flow. When the temperature reached the target temperature, the furnace tube was evacuated to a base pressure of 8 × 10−3 Torr. Then, the furnace tube was kept at a constant temperature and pressure condition for a controlled time (90~120 min). At the end of the growth process, the tube was thoroughly purged with a constant Ar flow and cooled down slowly.
CdTe/CdS Hierarchical Nanostructure Growth
Firstly, single-crystalline CdS NWs were grown on a catalyst-coated SiO2 substrate using a VLS method. The CdS powder source was placed at the center of the alumina tube, and the substrates with Au catalyst film were placed at the downstream position of the source material. After evacuating the tube (base pressure of 10−6 Torr) and purging it with high-purity argon (Ar) for 90 min, the furnace was rapidly heated to 650 °C under a constant Ar flow with its flow rate of 300 sccm. When the temperature reached 650 °C, the tube was evacuated to the base pressure, and then, the tube was kept at this temperature for 40 min. After 40 min, the tube was purged with high-purity Ar gas with a constant flow rate of 300 sccm. Lastly, the tube was slowly cooled down to room temperature. For the growth of hierarchical nanostructures, an 8-nm-thick Au film was directly coated on the as-grown CdS NWs by thermal evaporation. Then, CdTe nanostructures were grown on the CdS NWs using the same method as described above.
Fabrication Process of Photodetectors Based on Hierarchical Nanostructures
The as-grown CdTe NWs or CdTe/CdS hierarchical nanostructures were dispersed in anhydrous ethanol by ultra-sonication for ~2 min. And then, using a drop and evaporation process, the individual NWs or the hierarchical nanostructures were adsorbed on a clean bare SiO2 substrate. Lastly, metal electrodes (Au/Ti = 50 nm/10 nm) were fabricated by a conventional lift-off process.
Results and Discussion
Figure 1b shows a schematic diagram depicting the fabrication of hierarchical nanostructures via secondary growth of CdTe nanostructures on CdS NWs. Firstly, single-crystalline CdS NWs were grown on a catalyst-coated SiO2 substrate using a previously reported VLS method [12, 13, 14]. The detailed process is described in our previous report . For the growth of hierarchical nanostructures, an 8-nm-thick Au film was directly coated on the as-grown CdS NWs by thermal evaporation. Then, CdTe nanostructures were grown on the CdS NWs using the same method shown in Fig. 1a. Note that since we utilized a high-temperature VLS method to grow the secondary nanostructures, the number of impurities at the interface between CdS NWs and CdTe nanostructures should be minimal, which is advantageous in improving the optoelectronic performance of our hierarchical nanostructures [12, 14].
However, the NWs were quite short, and most of them were just in an initiation phase. Here, the length of the CdTe NWs could be extended by replacing the Bi catalyst with Au film catalyst. Figure 2c shows a SEM image of CdTe NWs grown at 460 °C using the mixed powder (CdTe:Bi = 10:1 weight ratio) as a source material and an 8-nm-thick Au film as a catalyst instead of Bi catalyst. Notably, the CdTe NWs had a much higher aspect ratio than pure CdTe NWs grown on Bi catalysts (Fig. 2b). On the other hand, the aspect ratio of CdTe NWs decreased as the growth temperature was increased up to 540 °C (Fig. 2d). Therefore, we chose 460 °C as the growth temperature for the synthesis of CdTe NWs with a high aspect ratio. As a control experiment, we have also grown CdTe nanostructures using Au catalyst and a pure CdTe powder source (without Bi powder). In this case, just a small number of NWs was grown as shown in Fig. 2e. The length and diameter of the NWs were not uniform, and the aspect ratio was very small. This result implies that Bi catalyst can make a huge difference in the morphology of the nanostructures as well as their structural uniformity during the growth of CdTe nanostructures . Similarly, it has been reported that the Bi powder induces the asymmetric crystallization of CdTe nanowires, which enabled the directional growth of NWs .
The average lengths of CdTe NWs grown under the different conditions are shown in Fig. 2f. This clearly shows that we can deliberately control the NW structures using different catalysts and growth conditions. In particular, it should be noted that we obtained the longest NWs when we used the Bi-assisted growth with Au catalyst.
Figure 2g shows the high-resolution transmission electron microscopy (HR-TEM) image of as-grown CdTe NWs (Fig. 2c). The NWs exhibited alloy droplets as nucleation seeds on their heads, which indicates that the NWs were actually grown by the VLS mechanism. The length of the NWs was several micrometers, and its diameter was about 60 nm. The TEM image shows the ~0.37-nm lattice fringe corresponding to the atomic planes along the  lattice direction. This result shows that our process allows us to grow highly crystalline CdTe NWs. The X-ray diffraction analysis suggests that the NWs had a cubic structure with the lattice parameter of a = 6.410 Å (Figure S1 in Additional file 1). The energy-dispersive X-ray spectroscopy (EDS) result of as-grown CdTe NWs (Fig. 2h) shows that the CdTe NWs were chemically pure, and the stoichiometric ratio was Bi:Cd:Te = 1:12:11.
A TEM image of a single as-grown branched CdTe/CdS NW is shown in Fig. 3c. The branched CdTe NWs were randomly oriented on the backbone CdS NW. The lattice fringe of the CdTe NWs was spaced by ~0.36 nm, which indicates the NWs had a high-quality crystalline structure. Figure 3d shows an EDS spectrum taken from our CdTe/CdS hierarchical nanostructures. Through EDS analysis, we could confirm that each of the CdS NWs and CdTe NWs was chemically pure and composed only of cadmium (Cd), sulfur (S), and telluride (Te) materials.
This process can be applied to various nanostructures other than CdTe/CdS NW hierarchical nanostructures. For example, we could also successfully fabricate CdS NW-CdS NW hierarchical structures (Figure S2 in Additional file 1), CdTe thin films, and CdTe NW-CdS nanobelt (NB) hierarchical structures (Figure S3 in Additional file 1).
Figure 4b shows the time response of a CdTe NW photodetector. A xenon lamp (300 W) and a mechanical chopper were used to provide the intensity-modulated input light, while a 1 V bias voltage was applied to the photodetector. Here, we measured the rise and fall times which were defined as the times required for the current to increase from 10 to 90 % of Ilight and decrease from 90 to 10 % of Ilight, respectively. In the case of the photodetector based on CdTe NWs, the measured rise time was 9.45 ms, and the fall time was 9.98 ms.
To enhance the relative photoresponsivity, we also fabricated photodetectors using CdTe/CdS hierarchical nanostructures. The fabrication method was similar to that of photodetectors based on a single CdTe NW. Figure 4c shows the I-V curves of the hierarchical nanostructure-based photodetector with or without light illumination. The measured photocurrent Ip was 0.29 and 1.65 μA at the bias voltage of −1.0 and +1.0 V, respectively. The relative responsivity of the photodetector based on hierarchical nanostructures exhibited values in the range of 30,000~80,000 % as shown in Fig. 4d. The detectivity was estimated as 8.585 × 1012 cm Hz1/2 W−1 and 4.039 × 1013 cm Hz1/2 W−1 at the bias voltage of −1.0 V and +1.0 V, respectively. Additionally, the photoconductive responses of the photodetectors based on the hierarchical nanostructures were also measured with different incident optical powers (Figure S5 in Additional file 1). It should be noted that all of these photoresponse performances such as the photocurrent, the detectivity, and the relative responsivity were quite improved compared to those of photodetectors based only on a single CdTe NW. Presumably, this extreme enhancement of the responsivity was due to the PNP type junction formed at CdTe NW (p-type)/CdS NW (n-type)/CdTe NW (p-type) interfaces. The PNP junction could decrease Idark more effectively, resulting in enhanced relative responsivity.
Additional file 1: Figure S6 shows the time response of the hierarchical nanostructure-based photodetector. This time response was measured using the same method as that used for the photodetector based on single CdTe NWs. When repeated light pulses with a frequency of 10 Hz were applied, the photodetector exhibited stable photoresponse without any degradation. Although this NW-based photodetectors did not show an ultra-fast responsivity, the stable response to a pulsed light source showed a possibility of using the CdTe/CdS hierarchical nanostructure as a component for practical photodetector applications.
The inset in Fig. 4d depicts the spectral response of the hierarchical nanostructure-based photodetector. For the measurement, a xenon lamp (100 mW cm−2) and a monochromator (Acton Research Corporation SpectraPro-150) were used to provide the monochromatic light with a wavelength ranging from 300 to 1100 nm. The photocurrent was measured at a 1 V bias voltage. The photocurrent was quite small for the light with its wavelength longer than 950 nm. When the wavelength approached values shorter than 950 nm, the photocurrent increased slowly and had a maximum value near 800 nm. This edge corresponds to the band-edge emission of CdTe NWs (Eg ≈ 1.5 eV, 827 nm, 300 K) , revealing that the photoconductivity was due to the electron-hole pairs generated by the incident light with a larger energy than the band gap. Unlike the spectral response of single CdTe NW-based devices , the increased photocurrent showed a plateau up to 400 nm and decreased beyond wavelength values shorter than 400 nm. Presumably, the absorption over a broad wavelength range in our devices was due to the heterojunction composed of CdTe and CdS NWs.
We developed a simple method to control the structure of CdTe NWs using Bi powder in a standard CVD process, which enabled the fabrication of NW-based hierarchical nanostructures with a largely enhanced photoconductivity. As a proof of concepts, we fabricated a photodetector based on CdTe/CdS hierarchical nanostructures. The hierarchical nanostructure-based photodetector showed a ~100 times higher photoresponsivity than photodetectors based only on a single CdTe NW. This improved photoconductivity is presumably due to the intrinsic PNP junction electronic structure of our branched NW-based hierarchical nanostructures. Our simple but efficient strategy should enable the fabrication of high-performance optoelectronic devices for versatile practical applications.
This work was supported by the Ministry of Science, ICT & Future Planning (2014M3A7B4051591). SH acknowledges the financial support from the NRF (2013M3C8A3078813, H-GUARD 2013M3A6B2078961). BYL acknowledges the financial support from the National Research Foundation (NRF) funded by the Korea Ministry of Science, ICT & Future Planning (Grant No. 2015R1A2A2A04002733, 2013R1A1A1010802). JJ acknowledges the support by the Natural Science Foundation for Distinguished Young Scholars of Xinjiang (Grant No. 2013711007) and NSFC (Grant No. 51472052). CL acknowledges the support by the Human Resources Development Program of the Korea Institute of Energy Technology Evaluation and Planning (KETEP) grant funded by the Korea Ministry of Trade, Industry and Energy (No. 20124010203170).
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