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Low-temperature synthesis of multilayer graphene/amorphous carbon hybrid films and their potential application in solar cells
Nanoscale Research Lettersvolume 7, Article number: 453 (2012)
The effect of reaction temperature on the synthesis of graphitic thin film on nickel substrate was investigated in the range of 400°C to 1,000°C. Amorphous carbon (a-C) film was obtained at 400°C on nickel foils by chemical vapor deposition; hybrid films of multilayer graphene (MLG) and a-C were synthesized at a temperature of 600°C, while MLG was obtained at temperatures in excess of 800°C. Schottky-junction solar cell devices prepared using films produced at 400°C, 600°C, 800°C, and 1,000°C coupled with n-type Si demonstrate power conversion efficiencies of 0.003%, 0.256%, 0.391%, and 0.586%, respectively. A HNO3 treatment has further improved the efficiencies of the corresponding devices to 0.004%, 1.080%, 0.800%, and 0.820%, respectively. These films are promising materials for application in low-cost and simple carbon-based solar cells.
Graphene has attracted widespread attention due to its unique band structure and fascinating electronic, optical, chemical, and mechanical properties [1–4]. Hybrid structures of graphene with other carbon materials such as carbon nanotubes (CNTs) [5, 6] and amorphous carbon (a-C)  could combine advantages of the constituent structures and find applications in many areas. For example, composites of a-C and graphene sheets exhibit attractive catalytic performance for the hydrolysis of cellohexaose . Multilayer graphene (MLG) oxide and a-C hybrid films were synthesized by incorporating MLG oxide into a-C matrix . The hybrid films show good electrical, mechanical, and tribological properties, with a sheet resistivity of approximately 100 Ω cm, Young’s modulus of 171 GPa, and elastic recovery of 81.4% . In addition, heterojunction solar cells based on carbon materials such as a-C films and graphene have attracted much attention . Their interesting optical properties, chemical inertness, and low cost make a-C films as potential candidate materials for solar cells [10, 11]. Indeed, carbon films were the earliest carbon materials partially replacing silicon (Si) in Si-based solar cells , but their poor electrical conductivity hinders their practical application . Excellent conductivity, good transparency, and high hole transport mobility make graphene as a promising candidate in photovoltaic devices [9, 13, 14]. Graphene/n-Si Schottky-junction solar cells have been assembled and demonstrated power conversion efficiencies up to 1.5% , but the fabrication process of the device is relatively complex because graphene easily cracks . Some of the above-mentioned shortcomings can be overcome by a graphene/a-C hybrid structure. Unfortunately, the reported method to prepare graphene/a-C hybrid structure involves several rigorous processing steps, including the fabrication of graphene oxide using expandable graphite, dissolving the graphene oxide into methanol, and electrolysis deposition of the methanol solution . Therefore, in situ graphene/a-C hybrid structure fabrication is highly desirable.
The synthesis of carbon nanomaterials (carbon nanotubes, graphene, carbon films, etc.) at a relatively low temperature is crucial for their practical applications [16, 17]. Firstly, a low temperature could simplify the growth process , and it is more convenient, cost-effective, and environment-friendly . Secondly, a low-temperature process is important for their electronic device applications . For example, complementary metal-oxide semiconductor (CMOS) technology is widely used in transistors. In CMOS technology, an oxide layer serves as an insulator between the transistor gate and the channel . In this sense, synthesis of carbon nanomaterials directly on certain substrates (e.g., oxide , nickel [13, 21]) is crucial. However, many substrates are vulnerable to heating ; thus, low-temperature synthesis of carbon nanomaterials would be attractive.
In this work, hybrid films of MLG and a-C were prepared at a relatively low temperature of 600°C. When the temperature exceeded 800°C, MLG is obtained. Schottky-junction solar cells based on n-type Si and 400°C, 600°C, 800°C, and 1,000°C samples demonstrate efficiencies of 0.003%, 0.256%, 0.391%, and 0.586%, respectively. After a HNO3 treatment, the efficiencies of the corresponding solar cells have further increased to 0.004%, 1.080%, 0.800%, and 0.820%, respectively. Our work has opened up a new avenue for the production of low-cost carbon-based solar cells in the future.
Synthesis of MLG
The experimental setup is similar to that for N-doped carbon films (N-CFMs) described in our previous work , except that H2 is used in this work. In addition, the substrate is also different from that of N-CFMs. Nickel (Ni) foil instead of copper foil is used as substrate for graphene growth. The Ni foil is mounted in the center of the quartz tube reactor and gradually heated up to the pre-determined temperature of 400°C, 600°C, 800°C, or 1,000°C in 100 min under the protection of an Ar flow of 300 ml/min. When the temperature reaches the set value, the Ni foil is further annealed for 30 min to homogenize the crystal grains and to remove the oxidation layers under a reducing atmosphere of Ar (2,000 ml/min) mixed with H2 (100 ml/min). Then, acetonitrile (CH3CN) is introduced into the reactor at a feed rate of 20 μl/min for 2 min under the reducing atmosphere of Ar (2,000 ml/min) and H2 (100 ml/min). Afterwards, the Ni foil is moved to the low-temperature region of the quartz reactor to achieve a fast cooling rate. To obtain freestanding films, the as-grown samples are treated in a mixed solution of 0.5 M FeCl3 and 0.5 M HCl. After being rinsed in distilled water for several times, freestanding films could be collected for further characterizations and device fabrication.
Characterization of samples
The morphologies of as-synthesized films were characterized using a transmission electron microscope (TEM, JEOL-2010, Akishima-shi, Japan). Raman spectra were obtained on a microscopic confocal Raman spectrometer (Renishaw RM 2000, Wotton-under-Edge, UK) with a 514.5-nm laser line. Optical transmission spectra were taken using a UV-2450 UV/Vis optical spectrometer (Shimadzu Corporation, Kyoto, Japan). Sheet resistances (Rs) of the samples were measured using a four-probe resistivity test system.
Solar cell device assembly
Heterojunction solar cells were assembled by covering the films synthesized at 400°C, 600°C, 800°C, and 1,000°C onto an n-type Si wafer with a square window of 3 mm × 3 mm surrounded by insulating silicon dioxide, and the detailed procedure of the cell assembling can be found in our previous report . The assembled solar cells were evaluated with a solar simulator (at AM 1.5, Newport, Irvine, CA, USA) and a Keithley 2400 SourceMeter (Cleveland, OH, USA).
The HNO3 treatment was carried out by exposing the as-synthesized films to HNO3 fumes. The assembled solar cell was placed above a vial containing fuming HNO3 (65 wt.%) for 60 s.
Results and discussion
An illustration of products synthesized at different temperatures and their typical Raman spectra are shown in Figure 1a,b, respectively. The spectra of all the products (Figure 1b) consist of three peaks at 1,350, 1,590, and 2,700 cm−1, which correspond to the D-band, G-band, and 2D-band, respectively. The D-band is activated usually by disorder and grain boundaries. It can be clearly seen from Figure 1b that the D-band becomes weaker as temperature increases, which indicates a decrease of defects with an increasing temperature. The G-band depends on the in-plane stretching motion and occurs for all sp2 carbon atom sites . Obvious G-band could be seen in products at all temperatures, which indicates the formation of sp2 carbon bondings. Sharp and symmetrical 2D-band is a typical feature of monolayer graphene [25, 26]. The full width at half maximum (FWHM) of a monolayer of graphene is approximately 30 cm−1, and the I2D/IG ratio is approximately 3 . There is a significant difference in the line shape of the 2D-band between samples obtained at low temperature (400°C and 600°C) and high temperature (800°C and 1,000°C). The 800°C and 1,000°C samples have a FWHM of 86 cm−1 and an I2D/IG ratio of approximately 0.45, showing the Raman feature of MLG . The 400°C and 600°C samples do not show obvious 2D-band. Furthermore, an obvious downshift of the 2D-band of the low-temperature samples (approximately 2,708 cm−1) could be seen, which should be compared with approximately 2,722 cm−1 for high-temperature ones. The difference of 2D-band between these samples is attributed to their difference in structures, which is confirmed by subsequent TEM measurements.
Typical TEM images of films produced at different temperatures are shown in Figure 2. Continuous films were obtained in all the cases (Figure 2a,c,e,g). In addition, there are many ball-like features on the surface of the films, which is similar with a previous report about MLG synthesis on Ni . Considering that the films mainly consist of carbon (XPS spectrum in Additional file 1: Figure S1), these balls are islands of a-C. Moreover, there is an obvious difference in the selected area electron diffraction (SAED) patterns of samples produced at different temperatures, as shown in Figure 2b,d,f,h. The SAED pattern of the 800°C and 1,000°C samples consists of diffraction spots attributable to graphene . The SAED pattern contains multiple spots, which could be caused by back-folding of edges, intrinsic rotational stacking faults, or overlapping domains of graphene layers . Both spots and rings are found in the SAED pattern of the 600°C sample. Since the films mainly consist of carbon, the diffraction spots can be attributed to MLG, and the rings, to a-C. This indicates that a hybrid structure of MLG and a-C is obtained at 600°C, which is also confirmed by scanning electron microscope (SEM) images and Raman spectra (Additional file 1: Figures S2 and S3). Only diffraction rings are found in the SAED pattern of the 400°C sample, indicating that the 400°C sample is an a-C film.
Different synthesizing temperatures resulted in different films. The reason could be explained as follows: The CVD growth of graphene on a transition metal consists of three stages: (1) precursor molecules collide with the metal surface; (2) carbon precursor molecules dehydrogenate and form active carbon species; and (3) active carbon species coalesce, nucleate, and grow to graphene . In stage 1, the temperatures do not have a significant effect on the reaction because the adsorption energies of organic precursors on the metal surface are very small (approximately 0.02 eV) . At stage 2, the activation energy of liquid organic precursor dehydrogenation is approximately 1.5 eV ; thus, a high temperature favors the formation of active carbon species. In stage 3, the high temperature is also beneficial for the graphene growth. At a low temperature, active carbon species lack the mobility to form crystalline carbon, and a more disordered form of carbon is formed .
The optical transmission spectra of the samples synthesized at different temperatures are shown in Figure 3a. Low-temperature samples possess better light transmittance than high-temperature ones. This can be attributed to their thickness difference. High temperature results in high C solubility in Ni ; thus, thicker films are supposed to be obtained at higher temperature. The thicknesses of the 600°C and 800°C samples are 25.4 ± 4.1 and 43.7 ± 2.0 nm, respectively (see AFM results in Additional file 1: Figure S4). The Rs values of samples obtained at different temperatures are measured using a four-probe resistivity test system. The Rs values of the 400°C, 600°C, 800°C, and 1,000°C samples are 9,564, 1,864, 346, and 262 Ω/sq, respectively. The difference in Rs between the films prepared at different temperatures is explained as follows:. Firstly, a thicker film forms at a higher temperature. This can be attributed to a higher C solubility in Ni at the higher temperature . The Rs of thin-film materials is inversely proportional to their thickness . Secondly, it can be seen from the SAED patterns of the four samples (Figure 2b,d,f,g) that high-temperature samples have a higher crystallization degree. This finding that a high temperature improves the crystallization is consistent with that of other reports of graphene synthesis on Ni . A better crystallization can lead to a lower Rs.
Schottky-junction solar cells are assembled using the 400°C, 600°C, 800°C, and 1,000°C samples and n-type Si. The detailed procedure of the cell assembly can be found in our previous work , and a schematic illustration of the solar cell configuration is shown in Figure 3b. The working mechanism of the Schottky-junction solar cells is illustrated using the 800°C sample (MLG). The energy band diagram of the forward-biased MLG/n-Si junction upon illumination is shown in Figure 3c. In this device configuration, MLG serves not only as a transparent electrode for light, but also as an active layer for electron–hole generation, separation, and hole transport. A space-charge region accompanied by V0 (built-in potential) is formed at the interface of MLG and n-Si because of their work function difference. The photogenerated holes (h+) and electrons (e−) are driven by V0 into the MLG and n-Si, respectively. The efficiency of the solar cell based on the 400°C sample is very low, resulting from its poor electrical conductivity. The current density (J) versus voltage (V) curves of the solar cell based on the 400°C sample is shown in Additional file 1: Figure S5. The J versus V curves of solar cells based on the 600°C, 800°C, and 1,000°C samples are shown in Figure 3d. The corresponding photovoltaic parameters, such as short-circuit current density (Jsc), open-circuit voltage (Voc), filling factor (FF), and power conversion efficiency (η), are listed in Table 1. As shown in Table 1, solar cells based on the 400°C, 600°C, 800°C, and 1,000°C samples demonstrate power conversion efficiencies of 0.003%, 0.256%, 0.391%, and 0.586%, respectively.
The power conversion efficiencies of the above-mentioned solar cells are very low, and our previous report had shown that a HNO3 treatment could enhance the efficiencies of CNT/n-Si solar cells . To the best of our knowledge, HNO3 treatment on MLG/a-C hybrid films had not been investigated yet. We believed that a HNO3 treatment may have a similar effect on the above-mentioned solar cells. After the HNO3 treatment, the efficiencies of the corresponding solar cells have improved to 0.004%, 1.080%, 0.800%, and 0.820%, respectively, as shown in Table 1. There are three main reasons for the efficiency improvement. Firstly, HNO3 doping could enlarge the work function of MLG ; thus, a higher Voc is obtained after HNO3 treatment (Table 1). Secondly, HNO3 modification enhances the sheet conductance of the films, leading to a larger Jsc. The Rs of the 400°C sample decreases from 9,564 to 8,572 Ω/sq, that of the 600°C sample decreases from 1,864 to 1,032 Ω/sq, that of the 800°C sample decreases from 346 to 282 Ω/sq, and that of the 1,000°C sample decreases from 262 to 208 Ω/sq. Thirdly, a HNO3 treatment could reduce the internal resistance of the solar cells ; thus, the FF is enhanced (Table 1).
The pristine cell efficiencies of the 800°C and 1,000°C samples are better than that of the 600°C sample, and it is interesting that after HNO3 treatment, the efficiency of the 600°C sample is better than that of the 800°C and 1,000°C samples. The reasons could be explained by the working mechanism of our Schottky-junction solar cells as follows: Firstly, 600°C, 800°C, and 1,000°C films serve as a transparent electrode for light, and the 600°C sample possesses better light transmittance. Compared with the 800°C and 1,000°C samples, more light reaches to the Schottky-junction interface of the 600°C sample, generating much more electron–hole pairs in the 600°C sample. Secondly, 600°C, 800°C, and 1,000°C films also serve as charge transport path. The electrical conductivity of the 600°C film is much poorer than that of 800°C and 1,000°C ones; thus, the electron–hole pairs could not be effectively separated and transported, resulting in a lower Jsc and power conversion efficiency. Thirdly, after HNO3 treatment, the electrical conductivities of 600°C, 800°C, and 1,000°C films are all improved, enhancing charge transport and Jsc. The 600°C sample generates much more electron–hole pairs, so the magnitude of the increase in Jsc is much larger than that associated with the 800°C and 1,000°C samples (Table 1), resulting in a better efficiency.
In summary, the temperature effect on the synthesis of graphitic thin film on Ni foil was investigated. It was observed that temperature was critical in the production of MLG and α-C films. At 400°C, a-C film was obtained on Ni foil by CVD. Hybrid film of MLG and a-C could be synthesized at 600°C, while MLG was obtained at 800°C and above. Schottky heterojunction solar cells based on 400°C, 600°C, 800°C, and 1,000°C samples and n-type Si demonstrated power conversion efficiencies of 0.003%, 0.256%, 0.391%, and 0.586%, respectively. HNO3 modification has improved the efficiencies by enhancing the sheet conductance and work functions of the as-synthesized samples. After the HNO3 treatment, the efficiencies of 400°C, 600°C, 800°, and 1,000°C devices could be increased to 0.004%, 1.080%, 0.080%, and 0.820%, respectively. Now, low-cost carbon-based window-layer materials have been synthesized and their efficiency can certainly be further improved. Also, carbon-based solar cells are easy to assemble. As such, the commercial production of this type of solar cells holds promise for the future.
Zhu YW, Murali S, Cai WW, Li XS, Suk JW, Potts JR, Ruoff RS: Graphene and graphene oxide: synthesis, properties, and applications. Adv Mater 2010, 22: 3906. 10.1002/adma.201001068
Soldano C, Mahmood A, Dujardin E: Production, properties and potential of graphene. Carbon 2010, 48: 2127. 10.1016/j.carbon.2010.01.058
Cui TX, Lv RT, Huang ZH, Zhu HW, Kang FY, Wang KL, Wu DH: Effect of feed rate on the production of nitrogen-doped graphene from liquid acetonitrile. Carbon 2012, 50: 3659. 10.1016/j.carbon.2012.03.038
Ehemann R, Krstic P, Dadras J, Kent P, Jakowski J: Detection of hydrogen using graphene. Nanoscale Res Lett 2012, 7: 198. 10.1186/1556-276X-7-198
Li CY, Li Z, Zhu HW, Wang KL, Wei JQ, Li XA, Sun PZ, Zhang H, Wu DH: Graphene nano-“patches” on a carbon nanotube network for highly transparent/conductive thin film applications. J Phys Chem C 2010, 114: 14008. 10.1021/jp1041487
Lv RT, Cui TX, Jun MS, Zhang QA, Cao AY, Su DS, Zhang ZJ, Yoon SH, Miyawaki J, Mochida I, Kang FY: Open-ended. N-doped carbon nanotube-graphene hybrid nanostructures as high-performance catalyst support. Adv Funct Mater 2011, 21: 999. 10.1002/adfm.201001602
Kitano M, Yamaguchi D, Suganuma S, Nakajima K, Kato H, Hayashi S, Hara M: Adsorption-enhanced hydrolysis of beta-1,4-glucan on graphene-based amorphous carbon bearing SO(3)H, COOH, and OH groups. Langmuir 2009, 25: 5068. 10.1021/la8040506
Zhang JY, Yu YL, Huang DM: Good electrical and mechanical properties induced by the multilayer graphene oxide sheets incorporated to amorphous carbon films. Solid State Sci 2010, 12: 1183. 10.1016/j.solidstatesciences.2010.03.017
Zhu HW, Wei JQ, Wang KL, Wu DH: Applications of carbon materials in photovoltaic solar cells. Sol Energ Mat Sol C 2009, 93: 1461. 10.1016/j.solmat.2009.04.006
Patsalas P: Optical properties of amorphous carbons and their applications and perspectives in photonics. Thin Solid Films 2011, 519: 3990. 10.1016/j.tsf.2011.01.202
Wang SF, Rao KK, Yang TCK, Wang HP: Investigation of nitrogen doped diamond like carbon films as counter electrodes in dye sensitized solar cells. J Alloys Compd 1969, 2011: 509.
Mukhopadhyay K, Mukhopadhyay I, Sharon M, Soga T, Umeno M: Carbon photovoltaic cell. Carbon 1997, 35: 863. 10.1016/S0008-6223(97)80177-7
Hu Y, Huo K, Chen H, Lu Y, Xu L, Hu Z, Chen Y: Field emission of carbon nanotubes grown on nickel substrate. Mater Chem Phys 2006, 100: 477. 10.1016/j.matchemphys.2006.01.029
Mohammed M, Li Z, Cui J, Chen TP: Junction investigation of graphene/silicon Schottky diodes. Nanoscale Res Lett 2012, 7: 302.
Reina A, Jia XT, Ho J, Nezich D, Son HB, Bulovic V, Dresselhaus MS, Kong J: Large area, few-layer graphene films on arbitrary substrates by chemical vapor deposition. Nano Lett 2009, 9: 30. 10.1021/nl801827v
Li ZC, Wu P, Wang CX, Fan XD, Zhang WH, Zhai XF, Zeng CG, Li ZY, Yang JL, Hou JG: Low-temperature growth of graphene by chemical vapor deposition using solid and liquid carbon sources. ACS Nano 2011, 5: 3385. 10.1021/nn200854p
Liao WH, Wei DH, Lin CR: Synthesis of highly transparent ultrananocrystalline diamond films from a low-pressure, low-temperature focused microwave plasma jet. Nanoscale Res Lett 2012, 7: 82. 10.1186/1556-276X-7-82
Vlassiouk I, Smirnov S, Ivanov I, Fulvio PF, Dai S, Meyer H, Chi MF, Hensley D, Datskos P, Lavrik NV: Electrical and thermal conductivity of low temperature CVD graphene: the effect of disorder. Nanotechnology 2011, 22: 275716. 10.1088/0957-4484/22/27/275716
Kim Y, Song W, Lee SY, Jeon C, Jung W, Kim M, Park CY: Low-temperature synthesis of graphene on nickel foil by microwave plasma chemical vapor deposition. Appl Phys Lett 2011, 98: 263106. 10.1063/1.3605560
Rummeli MH, Bachmatiuk A, Scott A, Borrnert F, Warner JH, Hoffman V, Lin JH, Cuniberti G, Buchner B: Direct low-temperature nanographene CVD synthesis over a dielectric insulator. ACS Nano 2010, 4: 4206. 10.1021/nn100971s
Du CS, Pan N: CVD growth of carbon nanotubes directly on nickel substrate. Mater Lett 2005, 59: 1678. 10.1016/j.matlet.2005.01.043
Kondo D, Sato S, Yagi K, Harada N, Sato M, Nihei M, Yokoyama N: Low-temperature synthesis of graphene and fabrication of top-gated field effect transistors without using transfer processes. Appl Phys Express 2010, 3: 025102. 10.1143/APEX.3.025102
Cui TX, Lv RT, Huang ZH, Zhu HW, Zhang J, Li Z, Jia Y, Kang FY, Wang KL, Wu DH: Synthesis of nitrogen-doped carbon thin films and their applications in solar cells. Carbon 2011, 49: 5022. 10.1016/j.carbon.2011.07.019
Koh ATT, Foong YM, Chua DHC: Cooling rate and energy dependence of pulsed laser fabricated graphene on nickel at reduced temperature. Appl Phys Lett 2010, 97: 114102. 10.1063/1.3489993
Ni ZH, Wang YY, Yu T, Shen ZX: Raman spectroscopy and imaging of graphene. Nano Res 2008, 1: 273. 10.1007/s12274-008-8036-1
Liu W, Li H, Xu C, Khatami Y, Banerjee K: Synthesis of high-quality monolayer and bilayer graphene on copper using chemical vapor deposition. Carbon 2011, 49: 4122. 10.1016/j.carbon.2011.05.047
Obraztsov AN, Obraztsova EA, Tyurnina AV, Zolotukhin AA: Chemical vapor deposition of thin graphite films of nanometer thickness. Carbon 2017, 2007: 45.
Robertson AW, Warner JH: Hexagonal single crystal domains of few-layer graphene on copper foils. Nano Lett 2011, 11: 1182. 10.1021/nl104142k
Singleton M, Nash P: The C-Ni (carbon-nickel) system. J Phase Equilib 1989, 10: 121.
Jia Y, Cao AY, Bai X, Li Z, Zhang LH, Guo N, Wei JQ, Wang KL, Zhu HW, Wu DH, Ajayan PM: Achieving high efficiency silicon-carbon nanotube heterojunction solar cells by acid doping. Nano Lett 2011, 11: 1901. 10.1021/nl2002632
Bae S, Kim H, Lee Y, Xu X, Park J-S, Zheng Y, Balakrishnan J, Lei T, Ri Kim H, Song YI, Kim Y-J, Kim KS, Ozyilmaz B, Ahn J-H, Hong BH, Iijima S: Roll-to-roll production of 30-inch graphene films for transparent electrodes. Nat Nano 2010, 5: 574.
We are grateful to the financial supports from the National Natural Science Foundation of China (grant nos. 50902080 and 50632040) and Guangdong Province Innovation R&D Team Plan (grant no. 2009010025).
The authors declare that they have no competing interests.
TC carried out most of the experiments and drafted the manuscript. RL participated in the manuscript preparation. ZH participated in the measurement of the optical transmission spectra. HZ participated in the revision of the manuscript. YJ and SC participated in the solar cell test. FK designed the experiments and revised the manuscript. KW and DW discussed and analyzed the experimental results. All authors read and approved the final manuscript.