- Nano Express
- Open Access
Improved Work Function of Poly(3,4-ethylenedioxythiophene): Poly(styrenesulfonic acid) and its Effect on Hybrid Silicon/Organic Heterojunction Solar Cells
Nanoscale Research Lettersvolume 11, Article number: 532 (2016)
Hybrid silicon/organic solar cells have been recently extensively investigated due to their simple structure and low-cost fabrication process. However, the efficiency of the solar cells is greatly limited by the barrier height as well as the carrier recombination at the silicon/organic interface. In this work, hydrochloroplatinic acid (H2PtCl6) is employed into the poly(3,4-ethlenedioxythiophene):poly(styrenesulfonate) (PEDOT:PSS) solution, and the work function (WF) of the PEDOT:PSS layer has been successfully improved. Based on the Pt-modified PEDOT:PSS layer, the efficiency of the silicon/PEDOT:PSS cell can be increased to 11.46%, corresponding to ~20% enhancement to the one without platinum (Pt) modification. Theoretical and experimental results show that, when increasing the WF of the PEDO:PSS layer, the barrier height between the silicon/PEDOT:PSS interface can be effectively enhanced. Meanwhile, the carrier recombination at the interface is significantly reduced. These results can contribute to better understanding of the interfacial mechanism of silicon/PEDOT:PSS interface, and further improving the device performance of silicon/organic solar cells.
Crystalline silicon solar cell has enjoyed years of success in the photovoltaic industry due to its excellent properties such as high power conversion efficiency (PCE) and long service life [1–4]. However, the fabrication of the crystalline silicon solar cell is quite complicated and high cost, since the conventional silicon p-n/p-i-n junction has to be formed at a high temperature process [5, 6]. To address the issue, hybrid silicon/organic solar cells, which combine good compatibility with the established silicon technology and the simple fabrication of organics, have been extensively investigated [7–11]. In particular, owing to the high transparence as well as the high conductivity of poly(3,4-ethylenedioxythiophene):poly(styrenesulfonate) (PEDOT:PSS), the hybrid silicon/PEDOT:PSS solar cell is a quite promising candidate for high-efficiency, low-cost photovoltaic application . Over the past years, various approaches have been employed to enhance the performance of this kind of devices, such as silicon surface passivation [13–17], surface morphology controlling [13, 18–21], and rear contact modification [22–25]. Considerable progress has been achieved for the silicon/PEDOT:PSS solar cell, and PCEs of over 11% have been reported by many groups [13, 23, 26–28]. Nevertheless, according to the simulation results, an ultimate PCE over 20% is theoretically possible for the silicon/PEDOT:PSS solar cells, and there are still much room for the performance improvement .
The silicon/PEDOT:PSS solar cell is generally assumed to be a Schottky junction solar cell, where the PEDOT:PSS serves as the metallic contact. In the cell, light is predominately absorbed by the silicon, and the generated electron-hole pairs are separated and swept into the proper directions by the driving force of the built-in potential (V bi) between the silicon/metal interfaces. It has been reported that increasing the V bi can successfully improve the silicon/PEDOT:PSS cell performance, such as inserting a high work function (WF) of hole transport layer of MoO3 or WO3 between the PEDOT:PSS layer and the top grid electrode [27, 30] and doping/undoping the rear contact [23, 25]. Fortunately, unlike the silicon/metal Schottky solar cells, where the barrier height of the silicon/metal is relatively insensitive to the WF of the metal owing to the formation of metal silicides during vacuum metal deposition on silicon , tuning the WF of PEDOT:PSS layer might be a direct and efficient approach to increase barrier height. By doping the PEDOT:PSS layer with perfluorinated ionomer (PFI), the WF of the layer has been increased about 0.3 eV, improving the PCE of the silicon/PEDOT:PSS cell form 8.2 to 9.9% .
Platinum (Pt) particles have attracted great attention due to its various potential applications, such as a catalyst in fuel cells and solar cells [33, 34] and charge storage medium in memory devices . Pt particles can be easily obtained by thermally decomposed of hexachloroplatinic (IV) acid (H2PtCl6) , which is one of the most readily available soluble compounds of Pt. In this work, we introduce H2PtCl6 to PEDOT:PSS solution and investigate its effect on the conductivity as well as WF of the fabricated PEDOT:PSS layer. Additionally, the effect on the device performance of corresponding silicon/organic solar cells is also explored. The results contribute to better understanding of the interfacial mechanism of silicon/PEDOT:PSS interface and further improving of the device performance of silicon/organic solar cells.
PEDOT:PSS solution (CLEVIOS PH 1000), Triton, and hydrochloroplatinic acid were purchased from Aldrich. Hydrofluoric acid (HF) and dimethyl sulfoxide (DMSO) were purchased from Sinopharm Chemical Reagent Co., Ltd., China and used as received. Deionized water (DI) with a resistance of 18 MΩ cm−1 was purified using a Nanopure Diamond system.
PEDOT:PSS Layer Fabrication
PEDOT:PSS solution (CLEVIOS PH 1000) was mixed with Triton (1 wt%) and DMSO (5 wt%). Additionally, in order to increase the WF of PEDOT:PSS layer, various volumes of hydrochloroplatinic acid (H2PtCl6), which was ~1 mg/ml in water, was also added. The volume ration of H2PtCl6 was 0, 5, 10 15, and 20%, respectively. The resulting solution was kept stirring for about 2 h and then spin-coated on the substrates at 2500 rpm for 1 min. After that, the layers were sintered at 180 °C for 15 min in a nitrogen atmosphere.
The clean n-type Si (100) substrates with resistivity of 1~3 Ω cm were methylated through a two-step chlorination/alkylation method [7, 36]. After that, PEDOT:PSS with different volume of H2PtCl6 were spin-coated on the silicon wafer at 2500 rpm for 1 min and then were heated at 180 °C for 15 min in a nitrogen atmosphere. The silver grid electrodes are thermally evaporated through a shadow mask with a 10 × 8 mm2 area, and the rear contact was obtained by vacuum thermal evaporating aluminum.
The film conductivity was obtained using a four-point-probe setup. The Kelvin probe miscrope images were recorded with a commercial AFM system (Veeco instruments MultiMode AFM with NanoScope IIIa controller and extender module) operating in LiftMode. X-ray diffraction (XRD) measurement is carried out using an X-ray powder diffractometer (PANAlytical Empyrean). The morphology of the films was observed using a scanning electron microscope (SEM, FEI/Quanta 200 FEG).
A Newport 91160 solar simulator equipped with a 300 W xenon lamp and an air mass (AM) 1.5 G filter was used to generate simulated solar spectrum irradiation source. The irradiation intensity was 100 mW cm−2 and calibrated by a Newport standard silicon solar cell 91150. The electrical data were recorded by a Keithley 2612 source meter. The capacitance was characterized with a Wayne Kerr 6500B impedance analyzer.
Results and Discussion
Characteristics of PEDOT:PSS Layers
In order to explore the effect of H2PtCl6, the conductivity as well as the WF of PEDOT:PSS layers fabricated with different volume of H2PtCl6 in water are investigated. Table 1 summarizes the conductivity as well as surface potential of the fabricated PEDOT:PSS layers. In the PEDOT:PSS solution, the conductive PEDOT grains are surrounded by the insulating PSS shells. After mixing with H2PtCl6, the Pt compound with a negative charge can be easily adhered onto the PEDOT grains that present a positive charge. Since H2PtCl6 can be thermally decomposed into Pt particles after sintering, the formed Pt particles are dispersed in PEDOT:PSS layer. Due to the same charge properties (Pt compound vs. PSS shell), the Pt compound can avoid agglomeration upon two aqueous solutions mixing under stirring. As shown in Fig. 1a, the formed Pt particles can be well dispersed in PEDOT:PSS layers without clear aggregation. Additional file 1: Figure S1 shows the XRD spectra of PEDOT:PSS layers fabricated without and with H2PtCl6. The decreased peaks suggest that the crystallinity of PEDOT:PSS layers with H2PtCl6 is reduced. Thus, with the H2PtCl6 addition, the conductivity of the fabricated PEDOT:PSS layer is decreased. When the volume ration is 10%, the conductivity of the layer decreases from 465 to 427 S/cm.
Where e is the elementary charge and the V CPD is the surface potential directly measured by SKPM [37, 38]. The WF variation can be easily observed by comparing the difference of V CPD. Figure 2 shows the V CPD of PEODOT:PSS layers fabricating with different volumes of H2PtCl6. It can be observed that the V CPD becomes more negative along the increasing volume of H2PtCl6. Here, the decrease of V CPD indicates a corresponding increase of WF. When the volume ration is 15%, the V CPD of the layer decreases from ~160 mV of the pristine layer to ~-150 mV, which means the WF of the layer increases about 310 mV. There are two possible reasons for the enhanced WF. First, H2PtCl6 can be thermally decomposed to Pt particles with high WF, and doping into the PEDOT:PSS layer can directly enhance the WF of PEDOT:PSS layer. Second, during the Pt particles formation, the density of PSS shells in the film increased. Additional file 1: Figure S2 shows the absorption spectra of PEDOT:PSS films without and with H2PtCl6. The absorption peaks at 193 and 225 nm are assignable to π−π* transitions of the PSS benzene ring , the increase of peak absorption for PEDOT:PSS layer modified with Pt particles indicates an increase in PSS concentration, which can also increase the WF of the PEDOT:PSS layer .
In previous report, when PEDOT:PSS was mixed with HAuCl4, both of the conductivity and WF of the PEDOT:PSS layer were increased . However, in present study, though the WF of the PEDOT:PSS layer is enhanced, the conductivity of the layer is reduced. The difference may origin from the large formed particles in the layer. As shown in Additional file 1: Figure S3, the diameter of the formed particle is ~200 nm, which could disturb and inhibit 3-dimensional connections between the conducting PEDOT chains [42, 43]. AFM images of PEDOT:PSS layers fabricated with and without H2PtCl6 have also been measured as shown in Fig. 3. It can be observed that surface of PEDOT:PSS layers with and without Pt particles are similar, and the size of the formed Pt particles in PEDOT:PSS layer is consistent with that of SEM image (Additional file 1: Figure S3).
Device Performance for Hybrid Silicon/PEDOT:PSS Cells
Figure 4 shows the current density (J) vs. voltage (V) characteristics of the hybrid silicon/PEDOT:PSS devices fabricating with different volumes of H2PtCl6 under AM1.5 simulated illumination at 100 mW cm-2. The electric output characteristics of short-circuit current density (J SC), open-circuit voltage (V OC), fill factor (FF), and PCE are summarized in Table 2. It could be observed that the performance of devices improve first along the volume ration, peaking at 10% with a PCE of 11.46% which corresponds to ~20% improvement. It should be noted that though the WF of PEDOT:PSS layer is increased along the volume of H2PtCl6, the conductivity of PEDOT:PSS layer is reduced. At the low volume of H2PtCl6, this potential drawback can be overwhelmed by the advantage resulting from the enhanced WF, which means employing large V bi for charge separation and collection. Thus, the enhancement of the device performance mainly originates from the increase in FF and V OC, from 0.628 to 0.692 and 0.541 to 0.580 V, respectively. Further increasing the volume, the performance of the device gets degraded. There are two possible reasons for this phenomenon. First, in addition to the decreased conductivity, as shown in Additional file 1: Figure S4, big clusters of particles are formed which could promote carrier recombination between the layer and the metal electrode. Second, the layer roughness which results from the increased Pt particles is also increased. The rougher surface could cause the difficulty of the uniform formation of the Ag electrodes during the thermal evaporation, increasing the contact resistance between the layer and Ag electrode . As a result, when the volume ration of H2PtCl6 is higher, the performance of the devices is reduced.
Notably, when the PEDOT:PSS solution is mixed with H2PtCl6 in water, the layer thickness is decreased. In order to investigate the effect of thickness on the devices, we can compare the devices without or with the water addition. According to the results of the devices with different volumes of H2PtCl6 (Fig. 4 and Table 2), the optimal volume ration is 10%. Here, adding 10% volume ration of water, the thickness of the PEDOT:PSS layer is decreased from 100 to 89 nm. Nevertheless, as shown in Additional file 1: Figure S5, the J-V characteristics of the devices are similar, the PCE of the device without and with water addition are 9.51% and 9.58%, respectively. No discernible difference in the performance is observed. Hence, we make sure the change is caused by H2PtCl6.
Electrical Effect of H2PtCl6
In the hybrid silicon/PEDOT:PSS devices, light is predominately absorbed by the silicon, the generated electron-hole pairs are separated and swept into the proper directions by the driving force of V bi. So, the V bi between the silicon/PEDOT:PSS interface is an important factor which should be high enough to guarantee the charge separation and collection, sweeping charge into the proper directions. Figure 5 illustrates the band energy diagram at the n-type silicon/PEDOT:PSS interface. According to an ideal Schottky-Mott model , the Schottky barrier height (Φ SBH) at the silicon/PEDOT:PSS interface is proportional to the difference between the WF and the electron affinity of silicon (χ Si) by an equation of eΦ SBH=WF−χ Si. Because the V bi is related to the Φ SBH via the expression of Φ SBH=V bi + e−1 kT ln(NC/ND), where N C is the effective density of states in the conduction band and N D is the doping level of the semiconductor. In our devices, methylation could successfully passivate the silicon surface, there could be no difference for N C and N D in the silicon substrates. Therefore, increasing Φ SBH means enhancing V bi. Improving the WF of PEDOT:PSS layer could successfully enlarge the Φ SBH/V bi of the device. After mixing with H2PtCl6, the WF of PEDOT:PSS layer is improved. In order to confirm the increase of Φ SBH/V bi resulting from the enhanced WF, we analyze the dark J-V data as shown in Fig. 6a with the help of the thermionic emission model :
Where J is the current density, J S is the reversed saturation current, A is the contact area, A * is the effective Richardson constant (≈252 A cm−2 K−2 for n-type silicon), T is the absolute temperature (298 K), k is the Boltzman constant, and n is the diode ideality factor. With the H2PtCl6 addition, the estimated Φ SBH of the hybrid silicon/PEDOT:PSS device increases from 0.783 to 0.856 V. In order to further confirm the increase of Φ SBH/V bi, the analysis of the C-V measurement is also used, which affords the information about the magnitude of V bi. According to Anderson’s model , the capacitance of the device can be described as 1/C 2∝(V bi−V) where C is capacitance, V is the applied voltage, and the value of V bi can be extracted from the extrapolation of the linear portion of the 1/C 2−V plots. As shown in Fig. 6b, the V bi value for the devices without and with H2PtCl6 are 0.69 and 0.77 V, respectively, showing 0.11 V increase. Both of the results coming from the dark J-V curves analysis and C-V measurement confirm that increasing the WF of PEDOT:PSS layer can successfully improve the Φ SBH/V bi of the silicon/PEDOT:PSS devices. Since the V OC of the silicon/PEDOT:PSS device is directly proportional to the V bi, the increase in V OC of the device with H2PtCl6 addition can be ascribed to the enhancement of V bi. In addition, enhancing the V bi is also beneficial for the charge separation and collection, largely reducing the recombination loss at the interface, thus the FF of the devices can be increased.
External quantum efficiency (EQE) measures the percentage of incident photons, those eventually result in free charges being collected through the electrodes. Factors beyond light absorption, such as the resistance of electrodes, charge separation, and collection efficiencies, will also affect the magnitude of EQE, which is not sensitive to the wavelength. Here, as shown in Fig. 6c, due to the enhancing charge separation and collection resulting from the improved V bi, the value of EQE spectrum device with H2PtCl6 is higher than that of device without H2PtCl6.
Minority Carrier Lifetime
To further investigate the silicon/PEDOT:PSS interface quality, we conduct a spatial mapping of minority carrier lifetime measurement for the samples. The lifetime mappings of the silicon/PEDOT:PSS samples without and with Pt particles are presented in Fig. 7, which correspond to an average lifetime of 74 and 84 μs, respectively. The increase of the average lifetime suggests that the effective minority carrier lifetime of the device can be improved with H2PtCl6 addition. Generally, the effective minority carrier lifetime of a silicon solar cell can be expressed as follows [13, 30]:
where t eff is the effective lifetime, t bulk is the bulk recombination lifetime, S is the surface recombination rate, and W is the wafer thickness. Since t bulk is fixed for the same silicon wafer, the increase of measured lifetime (t eff) reflects a lower surface recombination rate. The carrier recombination rate at the silicon surface is generally proportional to the population of electrons and holes. The introduction of H2PtCl6 can successively enhance the Φ SBH/V bi, which significantly reduces the population of electrons near the silicon surface and transfers them to the electrode; therefore, the carrier recombination at the silicon surface is largely reduced, resulting in the improvement of carrier lifetime. Note that the increase of carrier lifetime is expected to improve the J SC of the device. However, the J SC of the devices without and with H2PtCl6 has slight change. As mentioned above, there are two possible reasons for this point. One is that the slight decreased conductivity (465 S/cm without vs. 427 S/cm with H2PtCl6) of the layer, and the other is the rougher layer which is not beneficial for the charge transfer and collection. The competition between the increased carrier lifetime and the decreased conductivity as well as increased roughness of layer contributes to the slight JSC variation.
In summary, we have introduced H2PtCl6 to PEDOT:PSS solution, and the WF of the PEDOT:PSS layer has been successfully improved. The increased WF of Pt-modified PEDOT:PSS layer obviously enhances the Φ SBH as well as V bi of the silicon/PEDOT:PSS interface, which is beneficial for the charge separation and collection, and greatly suppresses the charge recombination at the silicon/PEDOT:PSS interface. As a result, the PCE of the hybrid silicon/PEDOT:PSS cell increases up to 11.46%, corresponding to ~20% enhancement to the one without Pt modification. Our results contribute to better understanding of the mechanism of silicon/PEDOT:PSS interface and further improving of the device performance of silicon/organic solar cells.
External quantum efficiency
- H2PtCl6 :
Power conversion efficiency
- V bi :
Oh J, Yuan HC, Branz HM (2012) An 18.2%-efficient black-silicon solar cell achieved through control of carrier recombination in nanostructures. Nat Nanotechnol 7:743–748
Garnett E, Yang P (2010) Light trapping in silicon nanowire solar cells. Nano Lett 10:1082–1087
Zhao J, Wang A, Green MA, Ferrazza F (1998) 19.8% efficient “honeycomb” textured multicrystalline and 24.4% monocrystalline silicon solar cells. Appl Phys Lett 73:1991–1993
Tyagi V, Rahim NA, Rahim N, Jeyraj A, Selvaraj L (2013) Progress in solar PV technology: research and achievement. Renew Sust Energ Rev 20:443–461
Kim DR, Lee CH, Rao PM, Cho IS, Zheng X (2011) Hybrid Si microwire and planar solar cells: passivation and characterization. Nano Lett 11:2704–2708
Lewis NS (2007) Toward cost-effective solar energy use. Science 315:798–801
Shen X, Sun B, Liu D, Lee ST (2011) Hybrid heterojunction solar cell based on organic–inorganic silicon nanowire array architecture. J Am Chem Soc 133:19408–19415
Shen X, Sun B, Yan F, Zhao J, Zhang F, Wang S, Zhu X, Lee S (2010) High-performance photoelectrochemical cells from ionic liquid electrolyte in methyl-terminated silicon nanowire arrays. ACS Nano 4:5869–5876
Zhang F, Sun B, Song T, Zhu X, Lee S (2011) Air stable, efficient hybrid photovoltaic devices based on poly (3-hexylthiophene) and silicon nanostructures. Chem Mater 23:2084–2090
Avasthi S, Lee S, Loo YL, Sturm JC (2011) Role of majority and minority carrier barriers silicon/organic hybrid heterojunction solar cells. Adv Mater 23:5762–5766
Shen X, Chen L, Li J, Zhao J (2016) Silicon microhole arrays architecture for stable and efficient photoelectrochemical cells using ionic liquids electrolytes. J Power Sources 318:146–153
Wright M, Uddin A (2012) Organic—inorganic hybrid solar cells: a comparative review. Sol Energy Mater Sol Cells 107:87–111
Yu P, Tsai CY, Chang JK, Lai CC, Chen PH, Lai YC, Tsai PT, Li MC, Pan HT, Huang YY (2013) 13% efficiency hybrid organic/silicon-nanowire heterojunction solar cell via interface engineering. ACS Nano 7:10780–10787
He L, Jiang C, Wang H, Lai D (2012) High efficiency planar Si/organic heterojunction hybrid solar cells. Appl Phys Lett 100:073503
Chi D, Qi B, Wang J, Qu S, Wang Z (2014) High-performance hybrid organic-inorganic solar cell based on planar n-type silicon. Appl Phys Lett 104:193903
Zhang F, Liu D, Zhang Y, Wei H, Song T, Sun B (2013) Methyl/allyl monolayer on silicon: efficient surface passivation for silicon-conjugated polymer hybrid solar cell. ACS Appl Mater Interfaces 5:4678–4684
Liu D, Zhang Y, Fang X, Zhang F, Song T, Sun B (2013) An 11%-power-conversion-efficiency organic–inorganic hybrid solar cell achieved by facile organic passivation. IEEE Electron Device Lett 34:345–347
Zhang F, Song T, Sun B (2012) Conjugated polymer–silicon nanowire array hybrid Schottky diode for solar cell application. Nanotechnology 23:194006
He L, Jiang C, Lai D, Wang H (2011) Highly efficient Si-nanorods/organic hybrid core-sheath heterojunction solar cells. Appl Phys Lett 99:021104
He L, Lai D, Wang H, Jiang C (2012) High‐efficiency Si/polymer hybrid solar cells based on synergistic surface texturing of Si nanowires on pyramids. Small 8:1664–1668
Kou YS, Yang ST, Thiyagu S, Liu CT, Wu JW, Lin CF (2016) Solution-processed carrier selective layers for high efficiency organic/nanostructured-silicon hybrid solar cells. Nanoscale 8:5379–5385
Zhang Y, Zu F, Lee ST, Liao L, Zhao N, Sun B (2014) Heterojunction with organic thin layers on silicon for record efficiency hybrid solar cells. Adv Energy Mater 4:2195–2223
Zhang Y, Cui W, Zhu Y, Zu F, Liao L, Lee ST, Sun B (2015) High efficiency hybrid PEDOT: PSS/nanostructured silicon Schottky junction solar cells by doping-free rear contact. Energ Environ Sci 8:297–302
Zhang Y, Liu R, Lee ST, Sun B (2014) The role of a LiF layer on the performance of poly (3, 4-ethylenedioxythiophene): poly (styrenesulfonate)/Si organic-inorganic hybrid solar cells. Appl Phys Lett 104:083514
Jeong S, Garnett EC, Wang S, Yu Z, Fan S, Brongersma ML, McGehee MD, Cui Y (2012) Hybrid silicon nanocone–polymer solar cells. Nano Lett 12:2971–2976
Thomas JP, Leung KT (2014) Defect‐minimized PEDOT: PSS/planar‐Si solar cell with very high efficiency. Adv Funct Mater 24:4978–4985
Mu X, Yu X, Xu D, Shen X, Xia Z, He H, Zhu H, Xie J, Sun B, Yang D (2015) High efficiency organic/silicon hybrid solar cells with doping-free selective emitter structure induced by a WO 3 thin interlayer. Nano Energy 16:54–61
Wu S, Cui W, Aghdassi N, Song T, Duhm S, Lee ST, Sun B (2016) Junction adhesion: nanostructured Si/organic heterojunction solar cells with high open-circuit voltage via improving junction quality. Adv Funct Mater 26:5192
Chen TG, Huang BY, Chen EC, Yu P, Meng HF (2012) Micro-textured conductive polymer/silicon heterojunction photovoltaic devices with high efficiency. Appl Phys Lett 101:033301
Liu R, Lee ST, Sun B (2014) 13.8% Efficiency hybrid Si/organic heterojunction solar cells with MoO3 film as antireflection and inversion induced layer. Adv Mater 26:6007–6012
Maldonado S, Knapp D, Lewis NS (2008) Near-ideal photodiodes from sintered gold nanoparticle films on methyl-terminated Si (111) surfaces. J Am Chem Soc 130:3300–3301
Zhu Y, Song T, Zhang F, Lee ST, Sun B (2013) Efficient organic-inorganic hybrid Schottky solar cell: the role of built-in potential. Appl Phys Lett 102:113504
Yoshitake T, Shimakawa Y, Kuroshima S, Kimura H, Ichihashi T, Kubo Y, Kasuya D, Takahashi K, Kokai F, Yudasaka M (2002) Preparation of fine platinum catalyst supported on single-wall carbon nanohorns for fuel cell application. Phys B Condens Matter 323:124–126
Fang X, Ma T, Guan G, Akiyama M, Kida T, Abe E (2004) Effect of the thickness of the Pt film coated on a counter electrode on the performance of a dye-sensitized solar cell. J Electroanal Chem 570:257–263
Lung H L, Hsieh K Y, Liu R, Wu T B, Tseng J Y (2005) Non-volatile memory cell having metal nano-particles for trapping charges and fabrication thereof. Google Patents. Macronix International Co., Ltd., Taiwan
Bansal A, Li X, Lauermann I, Lewis NS, Yi SI, Weinberg W (1996) Alkylation of Si surfaces using a two-step halogenation/Grignard route. J Am Chem Soc 118:7225–7226
Sun L, Wang J, Bonaccurso E (2010) Nanoelectronic properties of a model system and of a conjugated polymer: a study by Kelvin probe force microscopy and scanning conductive torsion mode microscopy. J Phys Chem C 114:7161–7168
Palermo V, Palma M, Samorì P (2006) Electronic characterization of organic thin films by Kelvin probe force microscopy. Adv Mater 18:145–164
Park S, Cho E, Song D, Conibeer G, Green MA (2009) n-Type silicon quantum dots and p-type crystalline silicon heteroface solar cells. Sol Energy Mater Sol Cells 93:684–690
Yeo JS, Yun JM, Kim DY, Park S, Kim SS, Yoon MH, Kim TW, Na SI (2012) Significant vertical phase separation in solvent-vapor-annealed poly (3, 4-ethylenedioxythiophene): poly (styrene sulfonate) composite films leading to better conductivity and work function for high-performance indium tin oxide-free optoelectronics. ACS Appl Mater Interfaces 4:2551–2560
Kim S, Kim HS, Park YD (2016) Doped PEDOT: PSS electrodes, patterned through wettability control, and their effects on the electrical properties of polymer thin film transistors. Org Electron 30:296–301
Jönsson S, Birgerson J, Crispin X, Greczynski G, Osikowicz W, Van Der Gon AD, Salaneck WR, Fahlman M (2003) The effects of solvents on the morphology and sheet resistance in poly (3, 4-ethylenedioxythiophene)–polystyrenesulfonic acid (PEDOT–PSS) films. Synth Met 139:1–10
Hwang J, Amy F, Kahn A (2006) Spectroscopic study on sputtered PEDOT · PSS: role of surface PSS layer. Org Electron 7:387–396
Sze SM, Ng KK (2006) Physics of semiconductor devices. Wiley.
Li X, Zhu H, Wang K, Cao A, Wei J, Li C, Jia Y, Li Z, Li X, Wu D (2010) Graphene‐on‐silicon Schottky junction solar cells. Adv Mater 22:2743–2748
This work was supported by the National Natural Science Foundation of China (51402128, 21504061, 51502116), the Natural Science Foundation of Jiangsu Province, China (No. BK20140561, BK20140557, BK20140311), the University Science Research Project of Jiangsu Province (No. 13KJB150033), and a project funded by Jiangsu University for Senior Intellectuals (No. 13JDG101). Thanks also should be expressed to Jiangsu Province for the support under the innovation/entrepreneurship program (Surencaiban 26).
Support of this work from the National Natural Science Foundation of China (No. 51402128, 21504061, 51502116) and the Natural Science Foundation of Jiangsu Province, China (No. BK20140561, BK20140557, BK20140311), University Science Research Project of Jiangsu Province (No. 13KJB150033), a project funded by Jiangsu University for Senior Intellectuals (No. 13JDG101), and Jiangsu Province for the support under the innovation/entrepreneurship program (Surencaiban 26 is acknowledged.
XS conceived and designed the study. LC and YH performed the experiments. XS, SL, and JZ wrote the paper. JP, SL, and JZ reviewed and edited the manuscript. All authors read and approved the final manuscript.
The authors declare that they have no competing interests.
Supplementary data. (DOC 183 kb)