# Electrical Characterization of Nanopolyaniline/Porous Silicon Heterojunction at High Temperatures

Authors: Salah E. El-Zohary; M. A. Shenashen; Nageh K. Allam; T. Okamoto; M. Haraguchi
Journal: Journal of Nanomaterials
 (2013)

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## Abstract

Nanopolyaniline/p-type porous silicon (NPANI/PSi) heterojunction films were chemically fabricated via in situ polymerization. The composition and morphology of the nanopolymer were confirmed using Fourier transform infrared, scanning electron microscopy, UV-visible, and transmission electron microscopy  techniques. The results indicated that the polymerization took place throughout the porous layer. TheI-V measurements, performed at different temperatures, enabled the calculation of ideality factor, barrier height, and series resistance of those films. The obtained ideality factor showed a nonideal diode behavior. The series resistance was found to decrease with increasing temperature.


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## Body

## 1. Introduction

Intrinsically conducting polymers, including polyacetylene, polyaniline (PANI), polypyrrole, polythiophene, poly(p-phenylene-vinylene), and so forth, are termed organic polymers that possess the electrical, electronic, magnetic, and optical properties that are close to that of metals. Besides, they keep the same mechanical properties, processability, and so forth that are commonly associated with conventional polymers. Therefore, these polymers are commonly known as “synthetic metals” [1]. PANI is one of the most important classes of conjugated polymers that possess excellent electronic, optical, and redox properties. Also, making PANI with acids improves its environmental stability and conductivity [2, 3]. PANI, as a conducting polymer, has been used in a plethora of practical applications such as battery electrodes [4, 5], electrochromic devices [6, 7], photoelectric cells [8], light-emitting diodes [9, 10], solar cells [11, 12], energy storage [13], electromagnetic interference shielding [14], electrostatic discharge [15], biosensors [16, 17], and anticorrosive coatings [18, 19].Various methods are available for the synthesis of PANI. However, the most widely used two techniques are electrochemical and chemical oxidative polymerization methods [20]. The chemical method is especially preferred as it can be used to produce PANI for large scale applications. Recently, there has been a great interest in the fabrication and assembly of nanostructured PANI, especially PANI nanofibers [21]. Since the first report by Huang et al. [22] that PANI nanofibers can be easily synthesized by an interfacial polymerization, many template-free methods have been established. For instance, PANI nanofibers were easily prepared by rapidly mixing acidic aqueous solutions of aniline and ammonium peroxydisulfate (APS) [23]. Also, nano-PANIs have been synthesized using dodecylbenzylsulfonic acid, which was successfully electrodeposited on the surface of glassy carbon electrodes to form nanostructured films suitable for heterogeneous catalysis applications [24].As another class of important materials, porous silicon (PSi) is commonly prepared by chemical or electrochemical dissolution of crystalline silicon in HF-based solutions. Electrochemically fabricated PSi has a set of unique properties, especially the open porous structure and the enormous surface area. Moreover, PSi is much more elastic and pliant than the starting Si and thus can be used as a buffer between Si substrates and growing epitaxial films [25, 26].Recently, there has been a great interest in the fabrication and assembly of organic/inorganic semiconductor heterostructures, which have been found promising in many applications, opening the door to new developments. For example, heterojunctions made of a thin layer of a molecular semiconductor deposited on the surface of an inorganic semiconductor substrate, such as Si, GaAs, or InP, have been found to form rectifiers with characteristics similar to ideal p-n junctions [27, 28]. Of special interest, PANI/Si heterojunction has recently been studied thoroughly. Wang and Schiff [29] fabricated heterojunction solar cells using PANI on crystalline Si. They found the open-circuit voltage to increase with increasing the conductivity of the PANI film, saturating at a value of 0.51 V. Dirani et al. [30] fabricated heterojunction diodes using poly(o-methoxyaniline)/PANI and amorphous/microcrystalline Si structures. They showed a dependence on the polymer doping level. Regarding the use of PSi, Chiboub et al. successfully prepared a PANI/PSi hybrid structure by oxidative chemical/electrochemical polymerization of an aniline-terminated PSi surface in the presence of aniline monomer in the solution. The results suggested that the PANI was covalently grafted onto the PSi surface, and that the polymerization took place throughout the porous layer. The resulting PANI/PSi hybrid interfaces showed a high chemical stability and good electrical properties [31]. Betty [32] presented an easy and inexpensive method for the fabrication of highly sensitive and specific immunosensor based on PANI/PS heterojunction. The PANI/PSi sensor was able to detect analyte-antibody interactions, while being reusable. A heterojunction between PSi and water-soluble copolymer of PANI was fabricated by Fan et al. [33], which showed rectifying characteristics that were enhanced with decreasing the degree of sulfonation and the thickness of the copolymer.As the operating temperature of the devices made of such heterojunctions is a determinant factor of their efficiency, Aydoğan et al. [34] studied the I-V characteristics of Au/PANI/PSi/Al heterostructure in a wide range of temperatures (90–300 K). They showed a decrease in the barrier height (BH) and an increase in the ideality factor (n) with decreasing temperature. The refractive index shows an anomalous dispersion in the absorption region and a normal behavior in the transparent region. Therefore, more studies are needed to evaluate the performance of such heterojunctions at different temperatures.Herein, we demonstrate the in situ chemical fabrication of nano-PANI/PSi heterojunction films and their characterization using FTIR, UV-visible, X-Ray, SEM, and TEM techniques. TheI-V characteristics of the films are studied at different temperatures (298–398 K) and discussed based on the thermionic model. The electronic parameters (e.g., n, BH, and resistance) of the fabricated heterostructures are also determined.


### 1.1. Materials

Aniline (Riedel-de Haën, puriss grade) was distilled twice under atmospheric pressure and over zinc dust before use. Ammonium peroxydisulfate (APS) (WINLAB, UK) and cetyltrimethylammonium bromide (CTAB) (Fluka) were used without further purification. Sulfuric acid (H2SO4) 96%, hydrogen peroxide (H2O2) 30% (Sigma-Aldrich), hydrofluoric acid (HF) 47–51% (Fluka), and ethanol and methanol were used as received.


### 1.2. Preparation of PSi Substrates

Double-side-polished p-type Si(100) wafer (boron-doped, 5–10 Ωcm resistivity) was first cleaned in 3 : 1 concentrated H2SO4/H2O2 for 5 min at 80°C and then sonicated in deionized water for 10 min. Consequently, the wafer was rinsed in acetone to remove the cleaning residue and acts as a further cleaning solvent, after that the wafer was immersed in methanol for 3 min to remove any acetone residue. Finally, the wafer was rinsed in deionized water for 3 min to remove methanol residue. The clean wafers were immersed in HF : H2O (1 : 10) solution for 20 s at room temperature to remove the native oxide. The hydrogen-terminated surfaces were electrochemically etched in a 1 : 1 : 3 (by volume) solution of HF : ethanol : H2O for 15 min. After etching, the samples were rinsed with ethanol and deionized water and then dried under a stream of dry nitrogen prior to use.


### 1.3. Preparation of PANI Nanoparticles/PSi Heterojunction

CTAB (0.05 g, 0.69 mM) was dissolved in doubly deionized water (40 mL) and stirred at room temperature. Aniline (0.05 M) was added to the CTAB solution and stirred for an additional one hour at room temperature (15±1°C). APS solution (0.0625 M) dissolved in deionized water (40 mL) was added to aniline solution at room temperature. Five mL of this mixture was then taken and poured carefully on the surface of PSi wafer. The remaining solution (75 mL) was left to complete the reaction. The originally colorless mixture turned blue and later became dark green. The resultant green color content was allowed to stand for 15 h without being disturbed. The solid mass was filtrated and washed with distilled water and methanol several times until the filtrate became colorless. The solid product was then dried in a vacuum oven at 60°C for 48 h to be ready for analytical measurements. Also, the wafer was washed with deionized water several times.


## 1.1. Materials

Aniline (Riedel-de Haën, puriss grade) was distilled twice under atmospheric pressure and over zinc dust before use. Ammonium peroxydisulfate (APS) (WINLAB, UK) and cetyltrimethylammonium bromide (CTAB) (Fluka) were used without further purification. Sulfuric acid (H2SO4) 96%, hydrogen peroxide (H2O2) 30% (Sigma-Aldrich), hydrofluoric acid (HF) 47–51% (Fluka), and ethanol and methanol were used as received.


## 1.2. Preparation of PSi Substrates

Double-side-polished p-type Si(100) wafer (boron-doped, 5–10 Ωcm resistivity) was first cleaned in 3 : 1 concentrated H2SO4/H2O2 for 5 min at 80°C and then sonicated in deionized water for 10 min. Consequently, the wafer was rinsed in acetone to remove the cleaning residue and acts as a further cleaning solvent, after that the wafer was immersed in methanol for 3 min to remove any acetone residue. Finally, the wafer was rinsed in deionized water for 3 min to remove methanol residue. The clean wafers were immersed in HF : H2O (1 : 10) solution for 20 s at room temperature to remove the native oxide. The hydrogen-terminated surfaces were electrochemically etched in a 1 : 1 : 3 (by volume) solution of HF : ethanol : H2O for 15 min. After etching, the samples were rinsed with ethanol and deionized water and then dried under a stream of dry nitrogen prior to use.


## 1.3. Preparation of PANI Nanoparticles/PSi Heterojunction

CTAB (0.05 g, 0.69 mM) was dissolved in doubly deionized water (40 mL) and stirred at room temperature. Aniline (0.05 M) was added to the CTAB solution and stirred for an additional one hour at room temperature (15±1°C). APS solution (0.0625 M) dissolved in deionized water (40 mL) was added to aniline solution at room temperature. Five mL of this mixture was then taken and poured carefully on the surface of PSi wafer. The remaining solution (75 mL) was left to complete the reaction. The originally colorless mixture turned blue and later became dark green. The resultant green color content was allowed to stand for 15 h without being disturbed. The solid mass was filtrated and washed with distilled water and methanol several times until the filtrate became colorless. The solid product was then dried in a vacuum oven at 60°C for 48 h to be ready for analytical measurements. Also, the wafer was washed with deionized water several times.


## 2. Characterization

### 2.1. UV-Visible Spectra

PANI films were obtained during the polymerization of aniline on rectangular glass slides. These slides were introduced into the reaction vessel before the polymerization starts. Once the reactants were introduced to the vessel, the film grows onto the glass support simultaneously. After time intervals during the polymerization process, the glass supports were removed from the reaction mixture and rinsed with deionized water and finally dried. These supports coated with PANI films were used for the UV-visible absorption measurements. The absorption spectra were recorded with a Shimadzu UV-2101 DC spectrophotometer. Uncoated glass supports were used as references.


### 2.2. FTIR Measurements

FTIR spectra of the PANI samples dispersed in a KBr pellet were obtained using a JASCO 410 instrument.


### 2.3. Scanning Electron Microscope (SEM)

A morphological study was performed via SEM observation of the cross section of PANI nanoparticles using a SEM (model JOEL14775) at 10 kV with gold coating on the samples.


### 2.4. Transmission Electron Microscopic Analysis (TEM)

The nanostructure of deposited PANI film was confirmed by TEM technique. TEM measurements were taken using a JEOL JEM-2000EX microscope at an accelerating voltage of 100 kV. For TEM observation, the PANI nanoparticles were placed onto a carbon film supported by a copper grid.


### 2.5.I-V Measurements

Current-voltage (I-V) characteristics of the heterojunction films were studied at different temperatures (298–398 K) using Keithley 2400 source meter. The temperature was continuously monitored by using thermocouple close to the sample.


## 2.1. UV-Visible Spectra

PANI films were obtained during the polymerization of aniline on rectangular glass slides. These slides were introduced into the reaction vessel before the polymerization starts. Once the reactants were introduced to the vessel, the film grows onto the glass support simultaneously. After time intervals during the polymerization process, the glass supports were removed from the reaction mixture and rinsed with deionized water and finally dried. These supports coated with PANI films were used for the UV-visible absorption measurements. The absorption spectra were recorded with a Shimadzu UV-2101 DC spectrophotometer. Uncoated glass supports were used as references.


## 2.2. FTIR Measurements

FTIR spectra of the PANI samples dispersed in a KBr pellet were obtained using a JASCO 410 instrument.


## 2.3. Scanning Electron Microscope (SEM)

A morphological study was performed via SEM observation of the cross section of PANI nanoparticles using a SEM (model JOEL14775) at 10 kV with gold coating on the samples.


## 2.4. Transmission Electron Microscopic Analysis (TEM)

The nanostructure of deposited PANI film was confirmed by TEM technique. TEM measurements were taken using a JEOL JEM-2000EX microscope at an accelerating voltage of 100 kV. For TEM observation, the PANI nanoparticles were placed onto a carbon film supported by a copper grid.


## 2.5.I-V Measurements

Current-voltage (I-V) characteristics of the heterojunction films were studied at different temperatures (298–398 K) using Keithley 2400 source meter. The temperature was continuously monitored by using thermocouple close to the sample.


## 3. Result and Discussion

### 3.1. Morphological, Structural, and Optical Properties

SEM was used to investigate the surface morphology of the NPANI synthesized in CTAB micelles. In the SEM micrographs (Figures1(a) and 1(b)), rod-like shape nanostructures can be distinguished (Figure 1(b)) with diameters ranging from 30–50 nm, which is in good agreement with the TEM results shown in Figure 2. The obtained diameters are much smaller with very narrow size distribution compared to those reported by Guo and Zhou who synthesized PANI nanofibers with diameters in the range 80–100 nm by electrochemical polymerization [35] and electrospun PANI with diameters of 20–150 nm [36]. However, these are larger than PANI nanofibers synthesized using aluminum oxide template (20–40 nm in diameter) [37] and FeCl3 as an oxidant (16–23 nm in diameter) [38]. In our study, the micelles formed by CTAB and aniline might act as templates for the formation of the obtained self-assembled PANI nanorods. Upon the addition of APS, polymerization takes place only at the micelle/water interface. In addition, as PANI is a rigid molecule, the micelles have a tendency to elongate in the direction of the polymer chain during the polymerization process resulting in the observed PANI nanorods.NPANI SEM micrographs and rod-like-shaped nanostructures.Figure 2
A TEM micrograph of synthesized rod-like NPANI.Figure3 represents the FTIR spectrum of the fabricated NPANI film. The characteristic sharp band that appeared at 1220–1020 cm−1 can be assigned to the C–N tertiary aromatic vibration, while the bands located at 1360, 1250, 1340, and 1310 cm−1 are due to the C–N primary and secondary vibrations. The sharp characteristic band at 3450–3200 cm−1 is due to the N–H stretching vibration. Moreover, the bands at 1550 and 1475 cm−1 are due to the presence of quinoid structure, and the band obtained at 1240 cm−1 can be related to the C–N stretching mode for the benzenoid ring. The band at 810 cm−1 is a characteristic of a p-substituted aromatic ring proposing that polymerization has proceeded in a “head to tail” form.Figure 3
FTIR spectrum of the synthesized NPANI.For more justification, Figure4 shows the UV-visible spectrum of NPANI film deposited on a glass substrate. It can be shown that the spectrum shows two bands; one at 345 nm corresponds to the π-π* transition of the benzenoid rings, and another broad band at 795 nm corresponds to the quinine structure.Figure 4
UV-visible spectrum of the synthesized NPANI.


### 3.2.I-V Measurements

According to the thermionic emission model, for a metal/semiconductor (M/S) or metal/polymer (M/P) contact [39–42], the I-V characteristic under the forward and reverse bias voltages through an SBD can be represented as
(1)I=I0(qVηKT)[1-exp(qVKT)],
where I is the forward diode current, I0 is the reverse saturation current, q is the electron charge, V is the applied bias voltage, k is the Boltzmann’s constant, T is the absolute temperature, and η is the ideality factor. The reverse saturation current (I0) can be obtained by extrapolating the linear portion of the forward bias in the ln I-V plot to the intercept point on the current axis at zero-bias (V = 0) and is given by
(2)I0=AA*T2exp(-qΦBkT),
where A is the effective diode area, A* is the effective Richardson constant (32 A/cm2K2 for p-type Si [43]), and ΦB is the zero-bias barrier height.The ideality factor (η), a dimensionless quantity, is a measure of the conformity of the diode behavior to pure thermionic emission. It is introduced to account for the deviation from the thermionic emission diffusion theory. η can be determined from the slope of the straight line region of the ln I-V plot and can be represented as
(3)η=qkT(dVd(lnI)).For an ideal diode,η is unity. However, values greater than unity are usually observed and attributed to many factors such as the presence of interfacial thin native oxide layer, series resistance, and so forth [44]. Also, barrier inhomogeneity has been used to explain the higher values of the ideality factor [9]. For the estimation of the barrier height (ΦB), one may also make use of the Richardson plot of saturation current, that is,
(4)ln(I0T2)=ln(AA*)-qΦBoKT.Based on the above analysis, theI-V measurements were done for the NPANI/PSi films to determine the transport mechanism in such diodes. Figure 5 shows the I-V characteristics under the forward and reverse bias conditions at different temperatures in the range 298–373 K. The curves are similar to that of a metal/semiconductor (MS) Schottky barrier (SB). Asymmetrical I-V characteristic under the forward and reverse bias voltages is observed. In the low voltages range, the forward current increases with increasing temperature indicating a negative resistance temperature coefficient. The observed exponential dependence may be due to the formation of a depletion region between NPANI layer and PSi film.Figure 5
I-V characteristics of NPANI/PSi heterojunction at different temperatures.It is observed that the junction exhibits strong rectifying characteristics in dark showing an n-p heterojunction as diode behavior. This behavior can be attributed to the barrier at the interface that limits the forward and reverse carriers flow across the junction, where the built-in potential could be developed [39]. The forward I-V characteristics of NPANI/PSi SB diode, according to thermionic emission theory [40], are expressed by (1). As can be seen in Figure 5, the forward bias of the structure current is an exponential function of the applied bias voltage in the intermediate voltage regime (V≥0.35 V).To confirm that the thermionic emission is the operating conduction mechanism, the experimental values ofη and ΦB at each temperature were determined using (3) and (4), respectively. η is estimated from the slope of the linear region of the forward bias plot shown in Figure 6. The obtained η values (2.8–5.45) indicate that the NPANI/PSi SBD represents a nonideal diode. Moreover, the obtained values (η>1) can be generally attributed to the presence of a bias-dependent Schottky barrier height “SBH.”Figure 6
ln
(
I
) vis bias voltage (V) for NPANI/PSi heterojunction at various temperatures in dark.For an inhomogeneous SBD, with a distribution of low SBH,η may increase with decreasing temperature [44]. The SB consists of laterally inhomogeneous patches of different barrier heights. Since current transport across the organic/inorganic interface is a temperature-activated process, at low temperature electrons are able to surmount the lower barriers and, therefore, the current transport will be dominated by the current flowing through the patches of lower SBH and larger η [39, 45, 46]. The high values of η are also probably due to a potential drop in the interface layer and presence of excess current as well as the recombination current through the interfacial states between the PSi substrate and the NPANI organic layer [44, 45]. In this case, ΦB is the contact potential barrier that exists at the interface between organic material and semiconductor layer.Using linear curve fitting of Figure6, ΦB was found to increase with increasing temperature, Figure 7, while η is decreasing with increasing temperature, in agreement with previous reports [34, 39]. It is important to note that such temperature dependence is an obvious disagreement with the reported negative temperature coefficient of SBHs.Figure 7
Temperature dependence of barrier height and ideality factor.Upon increasing the temperature, more and more electrons will have sufficient energy to surmount the higher barrier. As a result, the dominantΦB will increase with increasing temperature and bias voltage [40]. Therefore, the current flow through the lower ΦB and larger η will dominate the current transport mechanismFigure8 shows the variation of ΦB versus η for the tested PANI/PSi heterojunction. Note that a linear relationship between ΦB and η is obtained. This can be an evidence that the current transport across the organic/inorganic interface is a temperature-dependent activated process, which can be explained by lateral inhomogeneities of the barrier heights in the diodes [45].Figure 8
Barrier height versus ideality factor for the NPANI/PSi heterojunction.For the evaluation ofΦB, one may also make use of the Richardson plot of saturation current. Figure 9 shows the variation of ln(I0/T2) versus 1000/T where linear relation was observed over the entire range of temperature. This indicates that thermionic emission is the dominant mechanism of charge transport. A Richardson constant (A*) value of 2.8297 × 10−4 AK−2 cm−2 is determined from intercept at the ordinate of this experimental plot, which is much lower than the corresponding reported value (32 AK−2cm−2) for p-Si. This deviation may be due to the spatial inhomogeneous barrier heights and potential fluctuations at the interface that consist of low and high barrier areas [41, 42].Figure 9
Richardson plot for the NPANI/PSi heterojunction.According to the thermionic emission theory, the forward biasI-V characteristics of a Schottky diode with a series resistance can be approximately expressed as
(5)I=I0exp[q(V-IRs)ηkT],
where the IRs is the voltage drop across the series resistance (Rs) of the device. The series resistance can be determined using
(6)dVd(lnI)=ηkTq+IRs.The values of saturation current (I0), barrier height (ΦB), ideality factor (η), and Rs factor for NPANI/PSi heterojunction were calculated from the forward I-V characteristics at different temperatures and listed in Table 1.Table 1
Saturation current (I0), barrier height (ΦB), ideality factor (η), and Rs factor for NPANI/PSi heterojunction.
T  (K)
I
0  (A)
η
Φ
B  (eV)
d
V
/
d
(
ln
I
)
η
R
s  (kΩ)
298
8.52782 × 10−8
5.45
0.56
4.47
28.8
323
1.17942 × 10−7
3.95
0.60
3.34
16.8
348
1.83184 × 10−7
3.33
0.64
2.78
10.2
373
2.91448 × 10−7
2.80
0.67
2.24
5.81A plot of (dV/dlnI) versus (I) is linear with the slope giving the Rs, and η can be estimated from the intercept (ηkT/q). Temperature dependence of the obtained Rs is shown in Figure 10. The Rs values vary exponentially with temperature in the temperature range 298–398 K. The decrease in Rs with increasing temperature can be attributed to the factors responsible for increasing η and/or to the lack of free carriers at low temperatures [47].Figure 10
d
V
/
d
(
ln
I
)
-
I curves of the NPANI/PSi heterojunction at different temperatures.


## 3.1. Morphological, Structural, and Optical Properties

SEM was used to investigate the surface morphology of the NPANI synthesized in CTAB micelles. In the SEM micrographs (Figures1(a) and 1(b)), rod-like shape nanostructures can be distinguished (Figure 1(b)) with diameters ranging from 30–50 nm, which is in good agreement with the TEM results shown in Figure 2. The obtained diameters are much smaller with very narrow size distribution compared to those reported by Guo and Zhou who synthesized PANI nanofibers with diameters in the range 80–100 nm by electrochemical polymerization [35] and electrospun PANI with diameters of 20–150 nm [36]. However, these are larger than PANI nanofibers synthesized using aluminum oxide template (20–40 nm in diameter) [37] and FeCl3 as an oxidant (16–23 nm in diameter) [38]. In our study, the micelles formed by CTAB and aniline might act as templates for the formation of the obtained self-assembled PANI nanorods. Upon the addition of APS, polymerization takes place only at the micelle/water interface. In addition, as PANI is a rigid molecule, the micelles have a tendency to elongate in the direction of the polymer chain during the polymerization process resulting in the observed PANI nanorods.NPANI SEM micrographs and rod-like-shaped nanostructures.Figure 2
A TEM micrograph of synthesized rod-like NPANI.Figure3 represents the FTIR spectrum of the fabricated NPANI film. The characteristic sharp band that appeared at 1220–1020 cm−1 can be assigned to the C–N tertiary aromatic vibration, while the bands located at 1360, 1250, 1340, and 1310 cm−1 are due to the C–N primary and secondary vibrations. The sharp characteristic band at 3450–3200 cm−1 is due to the N–H stretching vibration. Moreover, the bands at 1550 and 1475 cm−1 are due to the presence of quinoid structure, and the band obtained at 1240 cm−1 can be related to the C–N stretching mode for the benzenoid ring. The band at 810 cm−1 is a characteristic of a p-substituted aromatic ring proposing that polymerization has proceeded in a “head to tail” form.Figure 3
FTIR spectrum of the synthesized NPANI.For more justification, Figure4 shows the UV-visible spectrum of NPANI film deposited on a glass substrate. It can be shown that the spectrum shows two bands; one at 345 nm corresponds to the π-π* transition of the benzenoid rings, and another broad band at 795 nm corresponds to the quinine structure.Figure 4
UV-visible spectrum of the synthesized NPANI.


## 3.2.I-V Measurements

According to the thermionic emission model, for a metal/semiconductor (M/S) or metal/polymer (M/P) contact [39–42], the I-V characteristic under the forward and reverse bias voltages through an SBD can be represented as
(1)I=I0(qVηKT)[1-exp(qVKT)],
where I is the forward diode current, I0 is the reverse saturation current, q is the electron charge, V is the applied bias voltage, k is the Boltzmann’s constant, T is the absolute temperature, and η is the ideality factor. The reverse saturation current (I0) can be obtained by extrapolating the linear portion of the forward bias in the ln I-V plot to the intercept point on the current axis at zero-bias (V = 0) and is given by
(2)I0=AA*T2exp(-qΦBkT),
where A is the effective diode area, A* is the effective Richardson constant (32 A/cm2K2 for p-type Si [43]), and ΦB is the zero-bias barrier height.The ideality factor (η), a dimensionless quantity, is a measure of the conformity of the diode behavior to pure thermionic emission. It is introduced to account for the deviation from the thermionic emission diffusion theory. η can be determined from the slope of the straight line region of the ln I-V plot and can be represented as
(3)η=qkT(dVd(lnI)).For an ideal diode,η is unity. However, values greater than unity are usually observed and attributed to many factors such as the presence of interfacial thin native oxide layer, series resistance, and so forth [44]. Also, barrier inhomogeneity has been used to explain the higher values of the ideality factor [9]. For the estimation of the barrier height (ΦB), one may also make use of the Richardson plot of saturation current, that is,
(4)ln(I0T2)=ln(AA*)-qΦBoKT.Based on the above analysis, theI-V measurements were done for the NPANI/PSi films to determine the transport mechanism in such diodes. Figure 5 shows the I-V characteristics under the forward and reverse bias conditions at different temperatures in the range 298–373 K. The curves are similar to that of a metal/semiconductor (MS) Schottky barrier (SB). Asymmetrical I-V characteristic under the forward and reverse bias voltages is observed. In the low voltages range, the forward current increases with increasing temperature indicating a negative resistance temperature coefficient. The observed exponential dependence may be due to the formation of a depletion region between NPANI layer and PSi film.Figure 5
I-V characteristics of NPANI/PSi heterojunction at different temperatures.It is observed that the junction exhibits strong rectifying characteristics in dark showing an n-p heterojunction as diode behavior. This behavior can be attributed to the barrier at the interface that limits the forward and reverse carriers flow across the junction, where the built-in potential could be developed [39]. The forward I-V characteristics of NPANI/PSi SB diode, according to thermionic emission theory [40], are expressed by (1). As can be seen in Figure 5, the forward bias of the structure current is an exponential function of the applied bias voltage in the intermediate voltage regime (V≥0.35 V).To confirm that the thermionic emission is the operating conduction mechanism, the experimental values ofη and ΦB at each temperature were determined using (3) and (4), respectively. η is estimated from the slope of the linear region of the forward bias plot shown in Figure 6. The obtained η values (2.8–5.45) indicate that the NPANI/PSi SBD represents a nonideal diode. Moreover, the obtained values (η>1) can be generally attributed to the presence of a bias-dependent Schottky barrier height “SBH.”Figure 6
ln
(
I
) vis bias voltage (V) for NPANI/PSi heterojunction at various temperatures in dark.For an inhomogeneous SBD, with a distribution of low SBH,η may increase with decreasing temperature [44]. The SB consists of laterally inhomogeneous patches of different barrier heights. Since current transport across the organic/inorganic interface is a temperature-activated process, at low temperature electrons are able to surmount the lower barriers and, therefore, the current transport will be dominated by the current flowing through the patches of lower SBH and larger η [39, 45, 46]. The high values of η are also probably due to a potential drop in the interface layer and presence of excess current as well as the recombination current through the interfacial states between the PSi substrate and the NPANI organic layer [44, 45]. In this case, ΦB is the contact potential barrier that exists at the interface between organic material and semiconductor layer.Using linear curve fitting of Figure6, ΦB was found to increase with increasing temperature, Figure 7, while η is decreasing with increasing temperature, in agreement with previous reports [34, 39]. It is important to note that such temperature dependence is an obvious disagreement with the reported negative temperature coefficient of SBHs.Figure 7
Temperature dependence of barrier height and ideality factor.Upon increasing the temperature, more and more electrons will have sufficient energy to surmount the higher barrier. As a result, the dominantΦB will increase with increasing temperature and bias voltage [40]. Therefore, the current flow through the lower ΦB and larger η will dominate the current transport mechanismFigure8 shows the variation of ΦB versus η for the tested PANI/PSi heterojunction. Note that a linear relationship between ΦB and η is obtained. This can be an evidence that the current transport across the organic/inorganic interface is a temperature-dependent activated process, which can be explained by lateral inhomogeneities of the barrier heights in the diodes [45].Figure 8
Barrier height versus ideality factor for the NPANI/PSi heterojunction.For the evaluation ofΦB, one may also make use of the Richardson plot of saturation current. Figure 9 shows the variation of ln(I0/T2) versus 1000/T where linear relation was observed over the entire range of temperature. This indicates that thermionic emission is the dominant mechanism of charge transport. A Richardson constant (A*) value of 2.8297 × 10−4 AK−2 cm−2 is determined from intercept at the ordinate of this experimental plot, which is much lower than the corresponding reported value (32 AK−2cm−2) for p-Si. This deviation may be due to the spatial inhomogeneous barrier heights and potential fluctuations at the interface that consist of low and high barrier areas [41, 42].Figure 9
Richardson plot for the NPANI/PSi heterojunction.According to the thermionic emission theory, the forward biasI-V characteristics of a Schottky diode with a series resistance can be approximately expressed as
(5)I=I0exp[q(V-IRs)ηkT],
where the IRs is the voltage drop across the series resistance (Rs) of the device. The series resistance can be determined using
(6)dVd(lnI)=ηkTq+IRs.The values of saturation current (I0), barrier height (ΦB), ideality factor (η), and Rs factor for NPANI/PSi heterojunction were calculated from the forward I-V characteristics at different temperatures and listed in Table 1.Table 1
Saturation current (I0), barrier height (ΦB), ideality factor (η), and Rs factor for NPANI/PSi heterojunction.
T  (K)
I
0  (A)
η
Φ
B  (eV)
d
V
/
d
(
ln
I
)
η
R
s  (kΩ)
298
8.52782 × 10−8
5.45
0.56
4.47
28.8
323
1.17942 × 10−7
3.95
0.60
3.34
16.8
348
1.83184 × 10−7
3.33
0.64
2.78
10.2
373
2.91448 × 10−7
2.80
0.67
2.24
5.81A plot of (dV/dlnI) versus (I) is linear with the slope giving the Rs, and η can be estimated from the intercept (ηkT/q). Temperature dependence of the obtained Rs is shown in Figure 10. The Rs values vary exponentially with temperature in the temperature range 298–398 K. The decrease in Rs with increasing temperature can be attributed to the factors responsible for increasing η and/or to the lack of free carriers at low temperatures [47].Figure 10
d
V
/
d
(
ln
I
)
-
I curves of the NPANI/PSi heterojunction at different temperatures.


## 4. Conclusion

The morphological, structural, and optical properties of the fabricated nanopolyaniline (NPANI) were characterized by SEM, TEM, FTIR, and UV-visible techniques. Different parameters for the assembled NPANI/PSi heterojunction were calculated fromI-V measurements performed in the dark conditions in the temperature range 298–373 K. It has been found that while the zero-bias barrier height decreases, the ideality factor increases with decreasing temperature. This behavior has been attributed to particular distribution of barrier heights, barrier inhomogeneity, and interface states localized at the NPANI/PSi SBD. The calculated ideality factor (2.8–5.45) indicates that NPANI/PSi SBD represents a nonideal diode. The series resistance values are decreased with increasing temperature, which was attributed to the factors responsible for the increase in η and/or to the lack of free carriers at low temperatures. The results suggested that the NPANI was covalently grafted onto the PSi surface, and polymerization took place throughout the porous layer.



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*Source: 568175-2013-03-03.xml*