Abstract
In this work, three-dimensional (3D) radial heterojunction photodetectors (PD) were constructed over vertical crystalline Si nanowires (SiNWs), with stacked hydrogenated amorphous germanium (a-Ge:H)/a-Si:H thin film layer as absorbers. The hetero absorber layer is designed to benefit from the type-II band alignment at the a-Ge/a-Si hetero-interface, which could help to enable an automated photo-carrier separation without exterior power supply. By inserting a carefully controlled a-Si passivation layer between the a-Ge:H layer and the p-type SiNWs, we demonstrate first a convenient fabrication of a new hetero a-Ge/a-Si structure operating as self-powered photodetectors (PD) in the near-infrared (NIR) range up to 900 nm, indicating a potential to serve as low cost, flexible and high performance radial junction sensing units for NIR imaging and PD applications.
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Introduction
Photodetectors (PDs) with a broad spectral response from ultraviolet (UV)-visible to near infrared (NIR) have attracted great attentions for a wide range of applications, which include imaging, thermo-sensing, communications, environmental monitoring and security surveillance1,2,3,4,5,6,7. As we know, the NIR and IR light can penetrate deeper into the bio-tissue, compared to the visible light, and thus have greater application potential in noninvasive biological detector and medical treatment8,9,10,11. So far, various materials such as III-V compounds and group IV photonics12,13,14,15,16 are frequently used in NIR PD application. Among them, Ge and related alloy PDs have an advantage as they can be fabricated in CMOS-compatible process for achieving a broader detection range17,18,19. Recently, there are also increasing research interests and efforts devoted to incorporating NIR PDs as photovoltaic bio-stimulator and detectors20,21.
Hydrogenated amorphous silicon (a-Si:H) thin film material has been widely used in constructing various optoelectronic devices, such as solar cells, because of its low-cost, low temperature and scalable fabrication process by plasma enhanced chemical vapor deposition (PECVD)22,23,24. However, the light absorption of a-Si:H is limited to the wavelengths <750 nm (due to its wider bandgap of ~1.7 eV), which is insufficient for NIR light detection. In comparison, hydrogenated amorphous germanium (a-Ge:H) with a narrower bandgap energy of ~1.1 eV25 can be used to expand the NIR absorption spectrum, while the deposition of a-Ge:H can also be accomplished via a low-temperature PECVD process13,26. Recently, there are many research efforts to expand the NIR absorption range by mixing a-Si:H and a-Ge:H to form a-SiGe:H alloy, which however suffer from a high defect density in the alloy with a low carrier mobility27,28. Furthermore, though the lattice quality of a-Ge:H can be improved by tuning deposition parameters29, a-Ge:H thin film alone is usually too defective to serve as high quality light absorbing layer, particularly for high performance PD applications26,30,31. Meanwhile, a-Si:H and a-Ge:H hetero-interface is known to be a Type-II band alignment, which can help to facilitate the separation of photo-generated carriers. Therefore, reducing the thickness of a-Ge:H absorber layer to facilitate carrier extraction, and adopting an a-Si:H passivation layer (PAL) at the heterojunction interface have been regarded as efficient ways to improve photovoltaic performances. For instances, D. Lundszien and T. Y. Lee et al. showed that a-Si:H thin film as a PAL at the p/i interface can increase open circuit voltage of solar cells32,33. D. P. Pham et al. reported that depositing a thin a-Si:H PAL at the p/a-SiGe:H interface can reduce the interface defects and significantly improve device performance34.
On the other hand, the reduced a-Ge:H layer thickness (and thus a reduced light absorption) has to be compensated by other structural design in order to achieve a sufficient light harvesting performance. To this end, three-dimensional (3D) radial junction (RJ) solar cells35,36,37,38, constructed over silicon nanowires (SiNWs), are particularly advantageous as they can achieve a strongly enhanced light trapping effect that allows for the use of a thinner absorber layer to achieve a fast carrier separation and collection. More importantly, the light-induced degradation problem can also be suppressed in the a-Si:H RJ solar cells with a rather thin absorber layer thickness <100 nm, as witnessed in our previous works39,40,41. In addition, it has been recently shown that the 3D RJ units can be directly constructed over flexible Al foil substrates with an excellent mechanical robustness against repetitive bending42, making them ideal candidates for flexible NIR bio-photoelectric stimulations or detections43,44.
Herein, we develop a new 3D SiNW architecture that integrates the PAL/a-Ge:H/a-Si:H light absorber layer in a 3D radial heterojunction (RHJ) structure to establish a high-performance NIR PD. The presence of ultra-thin a-Ge:H with only 6 nm thick can expand the absorption spectral of devices to a wider wavelength range spanning from 300 nm to 1050 nm. In parallel, the PAL at the p-SiNWs/a-Ge:H interface can not only modify the band gap but also reduce significantly the interface defect state density. By adjusting the thickness of the passivation layer, a rapid NIR photodetection is demonstrated with a fast response time of 2.62 μs in the NIR region.
Method
Device fabrication
Fabrication of PIN RJ PDs: Before evaporating a thin tin (Sn) layer of 2 nm, the AZO (Al-doped ZnO, bottom electrode) glasses were cleaned in acetone, methanol and deionized water by ultrasonication. Then, the Sn layer was treated in PECVD system by H2 plasma for 5 min to form discrete Sn droplets for subsequent catalyzing vertical SiNWs upon the AZO surface. Then, p-type SiNWs with a typical length of 1 μm and a mean diameter of 30 nm-40 nm were formed via VLS model, with the introduction of silane (SiH4) and diborane dopant (B2H6) gases at 400 °C. In the next step, intrinsic a-Si:H absorber and n-type a-Si:H layers, with the thicknesses of around 80 nm and 10 nm were subsequently deposited upon the SiNWs cores at 150 °C, respectively. Finally, a transparent ITO layer (~70 nm) as the top electrode was deposited by magnetron sputtering (140 W, 700 s) around the RJ units. The transverse cross-sectional top-view was shown in Fig. 1e, PIN a-Si:H Radial junction.
Fabrication of RHJ a-Ge:H PDs: The process of SiNWs growth, n-type a-Si:H and ITO deposition processes were the same as PIN RJ solar cells, where the intrinsic a-Si:H absorber layer was replaced by a-Ge:H layer with the growth gas of Germane (GeH4). The transverse cross-sectional view was shown in Fig. 1e, PIN a-Ge:H Radial junction.
Fabrication of RHJ PAL/a-Ge:H/a-Si:H PDs: The process of SiNWs growth, n-type a-Si:H and ITO deposition were same as PIN RJ solar cell. The intrinsic absorber includes three layers: a-Si:H PAL, a-Ge:H layer and outer a-Si:H layer. The thickness of PAL (~35 nm, ~23 nm, ~12 nm, 0 nm) was changed with deposition time (30 min, 20 min, 10 min, 0 min). The thickness of a-Ge:H layer (~16 nm, ~6 nm, ~3 nm, 0 nm) was changed with deposition time (30 min, 10 min, 5 min, 0 min). The cross-sectional view was illustrated in Fig. 1e, PIN a-Si:H/a-Ge:H/a-Si:H Radial junction, the corresponding production process was shown in Fig. 1a–d.
Device characterizations
The Current Density-Voltage (J-V) Characterization: The J-V characteristics were measured with standard AM1.5 G illumination (Newport, Oriel Sol-1A), where the external quantum efficiency (EQE) was measured by QEX-10 measurement System, with a sweep step of 10 nm from 300 nm to 1100 nm. We manufactured mask with several 1.5 mm × 4 mm rectangular patterns on it, and electrode ITO was only deposited in the rectangular region during magnetron sputtering. As for the impact of beam spot size and position, the EQE measurement has been carried out with a spot size (~1.8 mm × 4 mm) that can cover around 80% of the ITO electrode area.
Response Speed Characterization: NIR Monochromatic (λ = 808 nm) spectrum was produced by a pulsed laser (MDL-H-808nm-4W-17091506). The frequencies of light source were modulated ranging from 5 Hz to 50 kHz. The response results were displayed through a Keysight DSOX3052A oscilloscope.
Results and Discussion
A typical SEM image of a randomly oriented of PIN RHJ PAL/a-Ge:H/a-Si:H heterojunction is shown in Fig. 2a. It is interesting to note that, while the multilayer thin film coating by PECVD can be quite conformal around the SiNWs, the deposition of ITO by magnetron sputtering is not so uniform, especially along the depth of standing RJ units, as shown in Fig. 2b. Among the random but mutual-crossed RJ units, there exist extra current paths, which can help to transport and collect the photo-current among the crossed RJs, that has been analyzed in our previous work42.
First and foremost it is worth noting that the J-V characteristics and performance parameters of PIN RJ PD (corresponding to the device with a-Ge:H film thickness equals to 0 nm) were presented in Fig. 3a,c respectively. A short circuit current density (Jsc) of ~14.46 mA/cm2, open circuit voltage (Voc) of ~698 mV, fill factor (FF) of ~61%, and power conversion efficiency (PCE) of ~6.2% were obtained for the PIN RJ PD. While as shown in Fig. 3b, the EQE of PIN RJ PD is almost zero with the wavelength longer than 800 nm, indicating extremely weak or no absorption of the NIR due to the large bandgap of a-Si:H. In order to extend the absorption range to the NIR, we fabricated PIN RHJ a-Ge:H PD with a single a-Ge:H absorber layer (named as PIN RJ a-Ge:H PD). As shown in Fig. 3a,c, the performance of the device is extremely poor, almost has no photovoltaic response. The main causes are related to these factors: there is defect-rich region in the a-Ge:H film as well as in p-SiNWs/a-Ge:H interface, what’s more, the valence band offset at the p/i interface where there is a trap for holes will degrade forward diffusion of holes (illustrated in Fig. 1f)29.
In order to passivate the interface states as well as to improve the band energy alignment, we added an a-Si:H thin film as a PAL between p-SiNWs and a-Ge:H film and optimized the thickness of a-Ge:H film (~16 nm, ~6 nm and ~3 nm) to get PIN RHJ PAL/a-Ge:H/a-Si:H PD. Compared with the PIN RHJ a-Ge:H PD, the J-V characteristics and EQE response of RHJ PAL/a-Ge:H/a-Si:H PD are obviously improved, as shown in Fig. 3a–c. The optimal thickness of a-Ge:H film is 6 nm, corresponding EQE response reaching ~10% at the wavelength of 808 nm, and Jsc still maintaining 12.67 mA/cm2. We attributed the improvement to that PAL decreases the interface defect density as well as acts as an electron blocking layer, which clearly presented in the energy band diagram shown in Fig. 1g. However, considerable deterioration of J-V characteristics and EQE response in infrared region were caused when the thickness of a-Ge:H film is thicker (16 nm) or thinner (3 nm), which mainly because there exits high defect state density in a-Ge:H film when it is too thick and the infrared absorption is insufficient when it is too thin. It is noticeable that better EQE response was obtained in near infrared region (800 nm~1050 nm) for PIN RHJ PAL/a-Ge:H/a-Si:H PD with 6 nm ultrathin a-Ge:H film.
We also analyzed the relationship between the thickness of PAL and NIR detection performance, as shown in Fig. 4a–c. The J-V characteristics and EQE response changed significantly with various thicknesses of PAL. Remarkably, when the thickness of PAL is of ~23 nm, the EQE can reach ~15% at the wavelength of 808 nm (Fig. 4b), corresponding Jsc of 13.9 mA/cm2 and Voc of 640 mV (shown in Fig. 4c), which are almost as better as that of the PIN RJ PD.
As shown in Fig. 4a–d, the thickness of PAL can affect the electrical characteristics and spectral characteristic of PIN RHJ PAL/a-Ge:H/a-Si:H PD significantly. This is mainly because a-Ge:H layer will absorb photons under near-infrared radiation and photo-generated electrons will drift easily from a-Ge:H film to n-a-Si:H layer under the built-in electric field. However, photo-generated holes will be trapped in the region of the a-Ge:H layer because of the hole well, as shown in Fig. 1g, and difficult to transport to p-SiNWs. Therefore, if the PAL gets too thick (~35 nm), the photo-generated holes will accumulate in the a-Ge:H region and hard to be collected by the inner electrode, If the PAL gets too thin (~12 nm), there will exist high defects density at the interface of a-Ge:H/p-SiNWs. Both of them will result in the decrease of photocurrent. Furthermore, as shown in Fig. 4b, by introducing a 23 nm thick PAL, a significant reduction in the dark-current to 10 nA at 0 V reverse bias is observed, This dark current is ~one order of magnitude less than the PDs fabricated without this PAL.
Therefore, only when the thickness of PAL is appropriate (~23 nm), the photo-generated holes in a-Ge:H region might reach the p-SiNWs by tunneling effect, thus improving the performance of PD.
Meanwhile, the light distributions of devices under incident light (550 nm and 808 nm) are simulated by COMSOL to reveal the underlying reasons for high NIR absorption performance of PIN RHJ PAL/a-Ge:H/a-Si:H PD. As seen in Fig. 2c, a strong light absorption was observed under the visible irradiation (550 nm) in the multi absorber layer. Noticeably, a weak light absorption can be found in ultrathin (less than 10 nm) a-Ge:H film under 808 nm, which suggests that the a-Ge:H layer is very sensitive to NIR. Furthermore, the simulation of absorption of PAL, outer a-Si:H layer and a-Ge:H layer are presented in Fig. 2d. We can find that the outer a-Si:H layer and PAL absorb well in the visible region, while a-Ge:H layer mainly captures infrared light. The absorption of the device reaches about 15% at 808 nm wavelength, which is close to the actually measured EQE of RHJ PAL/a-Ge:H/a-Si:H PD.
Response speed as one of the most import parameters reflects the carrier separation and recombination in the devices, which is widely used in the optical imaging and communication. To evaluate the response time, we employ a function generator equipped with an illumination light (808 nm, schematically illustrated in Fig. 5a), which can generate different frequencies (from 5 kHz to 50 kHz). As shown in Fig. 5b–d, the device shows a stable and reproducible response oscillogram at the frequencies of 5 kHz, 10 kHz and 50 kHz. The rise time (trise) and fall time (tfall) were extracted from the one cycle at 10 kHz with a value of 2.62/2.65 μs as presented in Fig. 5e, which is faster than the previous reported NIR PDs based on TMD, quantum-dot materials. A cutoff frequency (f3dB) of 3 dB bandwidth of 3D PIN RHJ Sandwich structure NIR PD can be determined by the following equation: f3dB = 0.35/trise, and the corresponding value of device is estimated to be 133 kHz. Further investigation of photovoltage as a function of frequency are depicted in Fig. 5f in which the relative of (Vmax − Vmin)/Vmax only decreases 11% at ultra-high pulse frequency of 30 kHz, which confirms that the 3D PIN RJ sandwich structure NIR PD shows a stability in the signal output and can work at an even higher frequency.
References
Boushel, R. et al. Monitoring tissue oxygen availability with near infrared spectroscopy (NIRS) in health and disease. Scand J Med Sci Sports 11, 213–222 (2001).
Wang, Z. et al. Development of Communication&Storage system for NIR Spectrometer based on ARM-linux. IEEE, 1281–1283 (2010).
Whitney, B. A. & Kenyon, S. J. Near-Infrared Imaging Polarimetry of Embedded Young Stars in The Taurus-Auriga Molecular Cloud. The Astrophysical Journal 485, 703–734 (1997).
Steiner, L. A. et al. Near-infrared spectroscopy can monitor dynamic cerebral autoregulation in adults. Neurocritical care 10, 122–128 (2009).
Wang, C. et al. A peptide-based near-infrared fluorescence probe for dynamic monitoring senile plaques in Alzheimer’s disease mouse model. Chin. Sci. Bull. 62, 1593–1601 (2017).
Wang, T. et al. NIR-to-NIR UCL/T1-weighted MR/CT multimodal imaging by NaYbF4:Tm@NaGdF4:Yb-PVP upconversion nanoparticles. Chin. Sci. Bull. 62, 903–912 (2017).
Ran, Y. & Li, X. TanSat: a new star in global carbon monitoring from China. Chin. Sci. Bull. 64, 284–285 (2019).
Chen, S. et al. Near-infrared deep brain stimulation via upconversion nanoparticle–mediated optogenetics. Science 359, 679–684 (2018).
Su, Y. et al. Gold nanoparticles-decorated silicon nanowires as highly efficient near-infrared hyperthermia agents for cancer cells destruction. Nano letters 12, 1845–1850 (2012).
Jung, S., Shin, J., Pi, K., Goo Y., Cho D. SiNWs-Neuron Stimulation Device Integrated with Silicon Nanowire-Based Photodetection Circuit on a Flexible Substrate. Sensors 16 (2016).
Parameswaran, R. et al. SiNWs-Photoelectrochemical modulation of neuronal activity with free-standing coaxial silicon nanowires. Nature nanotechnology 13, 260–266 (2018).
Chauhan, D. et al. Effects of Barrier Energy Offset and Gradient in ExtendedWavelength Infrared Detectors. IEEE 2 (2018).
Rogalski, A. Infrared detectors: an overview. Infrared Phys. Technol. 43, 187–210 (2002).
Guoqing Tong, H. L. et al. Enhancing Hybrid Perovskite Detectability in the Deep Ultraviolet Region with Down-Conversion Dual-Phase (CsPbBr3−Cs4PbBr6) Films. J. Phys. Chem. Lett. 9, 1592–1599 (2018).
Guoqing Tong, X. G. et al. Rapid, stable and self-powered perovskite detectors via a fast chemical vapor deposition process. RSC Adv. 7, 18224–18230 (2017).
Guoqing Tong, H. L. et al. Thin Films via Vapor Deposition for High-Performance Rigid and Flexible Photodetectors. Small 14(1702523), 1702521–1702528 (2017).
Tang, L. et al. Nanometre-scale germanium photodetector enhanced by a near-infrared dipole antenna. Nature Photonics 2, 226–229 (2008).
Richard, S. Mid-infrared photonics in silicon and germanium. Nature Photonics 4, 495–497 (2010).
Dushaq, G., Nayfeh, A. & Rasras, M. S. Metal-germanium-metal photodetector grown on silicon using low temperature RF-PECVD. Optics express 25, 32110–32119, https://doi.org/10.1364/OE.25.032110 (2017).
Fang, Y. et al. Texturing Silicon Nanowires for Highly Localized Optical Modulation of Cellular Dynamics. Nano letters 18, 4487–4492 (2018).
Jiang, Y. et al. Nongenetic optical neuromodulation with silicon-based materials. Nature Protocols 14, 1339–1376 (2019).
Shah, A. V. et al. Thin-film silicon solar cell technology. Prog. Photovolt: Res. Appl. 12, 113–142 (2004).
Carlson, D. E. & Wronski, C. R. Amorphous silicon solar cell. Appl. Phys. Lett. 28, 671–673 (1976).
Schropp, R. E. I., Zeman, M. Amorphous and Microcrystalline Silicon Solar Cells. Springer Science+Business Media, Llc (1998).
Kusian, W., Pfleiderer, H. & Gonzel, E. Electron and hole μτ products sligtly doped a-Ge:H films. J. Non-Cryst. Solids 137&138, 813–816 (1991).
Drüsedau, T. & Schröder, B. Optimization of process parameters for the deposition of improveda-Ge:H by dc magnetron sputtering. J. Appl. Phys. 75, 2864–2875 (1994).
Veldhuizen, L. W. et al. Optimization of hydrogenated amorphous silicon germanium thin films and solar cells deposited by hot wire chemical vapor deposition. Thin Solid Films 595, 226–230 (2015).
Wang, G., Shi, C., Zhao, L., Diao, H. & Wang, W. Fabrication of amorphous silicon–germanium thin film solar cell toward broadening long wavelength response. J. Alloys Compd. 658, 543–547 (2016).
Johnson, E. V. Pere Roca i Cabarrocas. Spectral response and field enhanced reverse current in a-Ge:H nip photodiodes. Sol. Energy Mater. Sol. Cells 91, 877–881 (2007).
Noll, G. R., Carius, R. & Fuh, W. Photoluminesence in hydrogenated amorphous germanium (a-Ge:H). Solid State Commun. 55, 117–120 (1985).
Payson, J. S. & Ross, R. C. Opitical and electronic properties of plasma deposited a-Ge:H. J. Non-Cryst. Solids 77&78, 579–582 (1985).
Lundszien, D., Finger, F. & Wagner, H. A-Si:H buffer in a-SiGe:H solar cells. Sol. Energy Mater. Sol. Cells 74, 365–372 (2002).
Lee, T., Son, W., Lee, S. & Choi, S. Fabrication, and Characteristics of Pin-Type a-SiGe:H Thin-Film Solar Cells with a-Si:H Buffer and Graded Absorption Layer. Mol. Cryst. Liq. Cryst. 586, 1–8 (2014).
Phama, D. P. et al. Role of a-Si:H buffer layer at the p/i interface and band gap profiling of the absorption layer on enhancing cell parameters in hydrogenated amorphous silicon germanium solar cells. Optik 136, 507–512 (2017).
Alet, P.-J., Yu, L., Picardi, G. & Palacin, S. Roca i Cabarrocas. In situ generation of indium catalysts to grow crystalline silicon nanowires at low temperature on ITO. J. Mater. Chem. 18, 5187 (2008).
Muskens, O. L. et al. Design of Light Scattering in Nanowire Materials for Photovoltaic Applications. Nano letters 8, 2638–2642 (2008).
Street, R. A., Qi, P., Lujan, R. & Wong, W. S. Reflectivity of disordered silicon nanowires. Appl. Phys. Lett. 93, 163109 (2008).
Müller, M., Ledinský, M., Kočka, J., Fejfar, A. & Červenka, J. Effects of nanowire size and geometry on silicon nanowire array thin film solar cells. Journal of Vacuum Science & Technology B, Nanotechnology and Microelectronics: Materials, Processing, Measurement, and Phenomena 36, 011401 (2018).
Misra, S., Yu, L., Foldyna, M. & Roca i Cabarrocas, P. High efficiency and stable hydrogenated amorphous silicon radial junction solar cells built on VLS-grown silicon nanowires. Solar Energy Materials and Solar Cells 118, 90–95 (2013).
Yu, L. et al. Understanding light harvesting in radial junction amorphous silicon thin film solar cells. Scientific reports 4, 4357 (2014).
Qian, S. et al. Full potential of radial junction Si thin film solar cells with advanced junction materials and design. Appl. Phys. Lett. 107, 043902 (2015).
Sun, X. et al. Firmly standing three-dimensional radial junctions on soft aluminum foils enable extremely low cost flexible thin film solar cells with very high power-to-weight performance. Nano Energy 53, 83–90 (2018).
Rogers, H. Electronics for the Human Body. IEEE 3 (2017).
Núñez, C. G., William, T. N., Polat, E. O. & Dahiya, R. Energy-Autonomous, Flexible, and Transparent Tactile Skin. Adv. Funct. Mater. 27, 1606287 (2017).
Acknowledgements
The authors acknowledge the financial support from the National Key Research and Development Program of China grants under Nos. 2016YFA0202102 and 2018YFA0209100, The Natural Science Foundation of Jiangsu Higher Education Institutions of China (16KJD510003 and 18KJB140014).
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Linwei Yu, Junzhuan Wang and Ling Xu proposed the idea and discussed about the results, Xiaolin Sun and Ting Zhang carried out the experiments and discussed together, Xiaolin Sun wrote the manuscript and revised by Junzhuan Wang and Linwei Yu.
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Sun, X., Zhang, T., Yu, L. et al. Three-dimensional a-Si/a-Ge radial heterojunction near-infrared photovoltaic detector. Sci Rep 9, 19752 (2019). https://doi.org/10.1038/s41598-019-56374-2
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DOI: https://doi.org/10.1038/s41598-019-56374-2
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