# Copper Incorporation into CdS Thin Films by Ionic Exchange in an Aqueous Solution Process at Room Temperature

Authors: E. Flores-García; M. A. Hernández-Landaverde; P. González-García; R. Ramírez-Bon
Journal: Journal of Spectroscopy
 (2018)

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## Abstract

Cadmium sulfide (CdS) thin films were deposited, on glass substrates, at 70°C for 120 min using an ammonium-free chemical bath deposition process. After deposition, the films were placed in a CuCl2 solution for 45, 60, 75, and 90 min, respectively, for their ion exchange, generating CdxCu1-xS films. The obtained films were analyzed by X-ray diffraction, Raman spectroscopy, X-ray wavelength dispersion spectrometry, and scanning electron microscopy. The reference CdS films showed a homogeneous appearance and a yellowish color; elapsing the immersion time, the films changed their color showing a greenish appearance. The X-ray analysis indicated that the CdS films developed a hexagonal structure with preferential orientation along the plane (002). During the ion exchange, a decrease in the intensity of the reflection (002) was observed as well as a slight displacement of this reflection towards higher values of 2θ derived from the substitution of Cd atoms by Cu atoms. The WDS analysis revealed that approximately 10% of the cadmium atoms were replaced by copper ones after 90 min of immersion.


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## Body

## 1. Introduction

During the last three decades, the development and application of novel semiconductor materials has increased considerably. This positive trend is because of the versatility of semiconductor materials, whose properties allow for a wide range of technological applications such as diodes, photodetectors, thermistors, varistors, transistors, and solar cells among others. Such versatility of the semiconductor materials is based on the possibility to modify their electrical properties either by doping or by exposing to heat, light, and other external excitations. This enables the application of semiconductor devices for amplification, switching, and energy conversion. Silicon based semiconductors were the first materials used in this type of devices, but due to their high manufacturing costs, this type of technology is expensive as a consequence. Therefore, different research groups have focused their attention on other alternative semiconductor materials like those of the II-VI group chalcogenides family, which includes ZnO, CdS, CdTe, CdO, and others as alternative materials [1].Metal chalcogenides, in thin film form, have been widely used in different applications as superconducting films, diamond-like films, magnetic films, microelectronic devices, surface modification, hard coatings, photoconductors, IR detectors, solar control, solar selective coatings, optical imaging, solar cells, optical mass memories, sensors, fabrication of large area photodiode arrays catalyst, and so on. [2]. Cadmium sulfide (CdS) is one of the most promising II-VI compounds because of its wide range of application in photovoltaic cell, optical filters and multilayer light emitting diodes, photodetectors, thin film field effect transistors, gas sensors, and transparent conducting semiconductor for optoelectronic devices [3]. Hence, CdS thin films have become an important material for their use as window layers in the fabrication of thin-film solar cells because of the presence of suitable photoconductivity, high optical transmittance in the visible and infrared regions, and compact and uniform morphology to avoid short circuit effects [4]. Several methods have been reported for the deposition of CdS films such as vacuum evaporation [5], sputtering [6], molecular beam epitaxy (MBE) [7], metal organic chemical vapor deposition (MOCVD) [8], electrodeposition [9], successive ionic layer adsorption and reaction (SILAR) [10], and chemical bath deposition (CBD) [11]. Among these, CBD is one of the most versatile techniques used for thin film growth because of its suppleness, relative low-cost operation, scaling, and high reproducibility [12]. In addition, the CBD technique is quite appropriate for the film deposition at large scale without the need of sophisticated infrastructure like high vacuum systems.Deposition of CdS films by CBD is based on the formation of a solid phase from the slow release of Cd2+ and S2− ions contained in an aqueous solution; subsequently, these ions condense on substrates suitably mounted within the precursor solution [13]. Also, it is known that most CdS films produced by the CBD technique exhibit a highly stable hexagonal phase with orientation preferential and growth columnar along the c-axis perpendicular to the substrate [14], introducing less grain boundaries parallel to the junction which can impede the flow of photogenerated excess carriers to the grid [15]. Nevertheless, different effects can take place during their coupling in semiconductor heterojunctions including delamination and diffusion.In particular, related phenomena with the copper atoms diffusion in CuxS/CdS heterojunctions have been widely studied since the 80s, focusing their attention in the partial or complete transformation of a CdS phase into a phase of CuxS [16–18]. Other studies have been performed about CdS thin films which are centered in the substitution of Cd atoms by copper atoms [19, 20], producing CdS : Cu films with tunable properties in a wide range through a suitable composition. Therefore, in this work, the effect of the incorporation of copper substitutional atoms within hexagonal structure of the CdS through ionic exchange process in aqueous solution containing copper ions at room temperature was studied. The effect of immersion time over structural, morphological, and chemical properties of reference CdS films was evaluated.


## 2. Experimental Details

### 2.1. Deposition of the CdS Thin Films

CdS thin films were deposited on commercial glass slides (26 × 75 × 1 mm) using an ammonia-free chemical bath deposition process. The precursor solution, for the deposition of the CdS films, was prepared using a method reported previously by our research group, which consists in the sequential mixture of 25 ml of 0.1 M CdCl2, 20 ml of 1 M sodium citrate (SC), 5 ml of 1 M KOH, 5 ml of solution pH 10 based borate to maintain constant pH value of solution during all deposition process, 10 ml of 1 M CS(NH2)2 (thiourea), and enough deionized water to complete a total volume of 100 ml [21]. Prior to deposition, glass substrates were cleaned using common detergent and water, rinsed with deionized water, and subsequently were placed in ultrasonic bath for 10 min using different solvents such as acetone, mixture of ethanol : xylene : acetone (ratio 1 : 1 : 1 in volume), and ethanol, respectively. Subsequently, five substrates were dried with high purity nitrogen gas and were placed vertically against the wall of 100 ml beaker, and then the precursor solution was transferred to the beaker and introduced into a heated bath at 70°C during 120 min approximately. Finally, the substrates were removed from precursor solution, rinsed with deionized water, cleaned with wet cotton, and dried with nitrogen gas to remove the leftover material that could not be adhered to the substrate.


### 2.2. Copper Incorporation

CdS thin films, with thickness near to 140 nm, were immersed in aqueous cationic solution (CuCl2) and removed after 45, 60, 75, and 90 min. Here, the CuCl2 solution contained 0.34 ppm of Cu2+. Finally, the samples were labeled as L1, L2, L3, and L4, respectively.


### 2.3. Structural and Optical Characterization

X-ray diffraction (XRD) patterns were recorded on a Rigaku Dmax 2100 diffractometer, using Seemann-Bohlin geometry and Cu targetλ=0.156nm. The Raman spectra were acquired at room temperature in the frequency range of 100–800 cm−1 using a micro Raman Dilor Labram II with an Ar laser (488 nm) as excitation source. The thickness of the thin films was measured in ten different points using a 3D optical microscope Contour GT-K0 in PSI mode. The morphology and compositional analysis, by wavelength-dispersive X-ray spectroscopy (WDS) of the samples, were carried out using an electron probe microanalysis JEOL JXA-8530F.


## 2.1. Deposition of the CdS Thin Films

CdS thin films were deposited on commercial glass slides (26 × 75 × 1 mm) using an ammonia-free chemical bath deposition process. The precursor solution, for the deposition of the CdS films, was prepared using a method reported previously by our research group, which consists in the sequential mixture of 25 ml of 0.1 M CdCl2, 20 ml of 1 M sodium citrate (SC), 5 ml of 1 M KOH, 5 ml of solution pH 10 based borate to maintain constant pH value of solution during all deposition process, 10 ml of 1 M CS(NH2)2 (thiourea), and enough deionized water to complete a total volume of 100 ml [21]. Prior to deposition, glass substrates were cleaned using common detergent and water, rinsed with deionized water, and subsequently were placed in ultrasonic bath for 10 min using different solvents such as acetone, mixture of ethanol : xylene : acetone (ratio 1 : 1 : 1 in volume), and ethanol, respectively. Subsequently, five substrates were dried with high purity nitrogen gas and were placed vertically against the wall of 100 ml beaker, and then the precursor solution was transferred to the beaker and introduced into a heated bath at 70°C during 120 min approximately. Finally, the substrates were removed from precursor solution, rinsed with deionized water, cleaned with wet cotton, and dried with nitrogen gas to remove the leftover material that could not be adhered to the substrate.


## 2.2. Copper Incorporation

CdS thin films, with thickness near to 140 nm, were immersed in aqueous cationic solution (CuCl2) and removed after 45, 60, 75, and 90 min. Here, the CuCl2 solution contained 0.34 ppm of Cu2+. Finally, the samples were labeled as L1, L2, L3, and L4, respectively.


## 2.3. Structural and Optical Characterization

X-ray diffraction (XRD) patterns were recorded on a Rigaku Dmax 2100 diffractometer, using Seemann-Bohlin geometry and Cu targetλ=0.156nm. The Raman spectra were acquired at room temperature in the frequency range of 100–800 cm−1 using a micro Raman Dilor Labram II with an Ar laser (488 nm) as excitation source. The thickness of the thin films was measured in ten different points using a 3D optical microscope Contour GT-K0 in PSI mode. The morphology and compositional analysis, by wavelength-dispersive X-ray spectroscopy (WDS) of the samples, were carried out using an electron probe microanalysis JEOL JXA-8530F.


## 3. Results and Discussion

### 3.1. Structural Properties

The CdS thin films obtained in this work presented uniform distribution on the substrate (observed by the eye), specular with light-yellow appearance and, also showed good adherence to the substrate. After immersion in the cationic solution, with the increase of the immersion time, the CdS films changed their appearance from yellowish to greenish color. This color change can be interpreted as the first evidence of the incorporation of copper atoms within crystalline structure of the cadmium sulfide. That is, Cu2+ ions can be incorporated into CdS thin films substituting Cd2+ by means of simple ion exchange process in aqueous solution, according to the following equation:(1)CdS+CuCl2⟶CuS+CdCl2where, the cations ligated within their crystal host lattice can be substituted with those present in the solution.Figure1 shows the X-ray patterns obtained for the different samples, here is included the CdS reference film labeled as L0. As observed, all the patterns show an intense diffraction peak at 2θ ≈ 26.7°, which could correspond to the (002) reflection of the CdS hexagonal phase or the (111) reflection of the CdS cubic structure. The predominance of this reflection in the XRD patterns indicates that the films are polycrystalline with high preferential orientation along the (002) or (111) crystalline direction. As well, the pattern of the CdS films show reflections located at 2θ ≈ 44 and 53° that can be assigned to the (220) and (331) crystalline planes of the cubic phase (JCPS #01-010-0454) or (110) and (112) planes of the hexagonal structure (JCPS #01-080-0006) of CdS, respectively. However, a reflection located at 2θ ≈ 48°, which explicitly corresponds to the (103) reflection of the hexagonal phase of CdS is also detected. Presence of this last reflection might suggest that the precursor solution used in this work favors the formation of a predominantly hexagonal phase. Similar outcomes have been reported by several research groups in CdS thin films obtained by chemical bath deposition in basic medium [22–24]. On the contrary, note that, in the XRD patterns for the samples L1, L2, L3, and L4, neither CuS nor Cu2S diffraction maxima are observed, indicating that these phases were not formed during the immersion process.Figure 1
XRD patterns set for CdS : Cu films obtained by ionic exchange process in aqueous solution. The inset in the upper-right zone is an enlargement around the (002) reflection.From the XRD analysis, we can observe two important effects in the principal (002) reflection as immersion time of the sample within the cationic solution increases: (i) it is slightly shifted to larger values of 2-theta and (ii) its intensity decreases. This can be explained as follows: the copper atoms present in the cationic solution can replace the Cd atoms ligated within the crystal lattice of the CdS, producing substitutional doping [25]. The observed structural changes originate from the difference between the ionic radius of both cations (Cu2+ = 87 pm and Cd2+ = 109 pm). According to Bragg’s law, the slight shift of the (002) diffraction peak towards larger values of 2-theta is related with the shrinkage of the c lattice constant of the hexagonal cell, which can be explained by the substitution of Cd cations by smaller Cu ones in the CdS crystalline lattice. On the contrary, the substitution of the Cd atoms by Cu atoms promotes disorder into the crystalline host cell; consequently, the width and intensity of the (002) peak is affected directly by the order-disorder effect [26, 27]. These phenomena can be explained as follows: when the CdS films are immersed into the cationic solution, the Cd atoms are displaced from the crystalline host cell destabilizing their structure (disorder effect); subsequently, the vacancy sites are occupied by Cu atoms stabilizing the crystal lattice again (order effect).The latter effect can be better observed in the inset of Figure1, where a meaningful decrease in the (002) reflection intensity is observed during the first 45 min immersion; afterward at 60 and 75 min, the (002) reflection intensity increases slightly, due to the reorder of the atoms as mentioned before. At 90 min, a decrease is observed again owing to direct substitution of Cd atoms by Cu atoms (Cu radius < Cd radius). This situation can be validated through the difference observed in the crystalline parameters of the CdS : Cu films, determined from XRD patterns, using the Jade 9.7 software™ (Table 1).Table 1
Cell parameters of CdS : Cu thin films obtained by XRD.
Sample
a (Å)
c (Å)
Cell volume (Å3)
Crystallite size (nm)
L0
4.1053
6.6802
112.58
26.2
L1
4.1053
6.6587
112.22
21.8
L2
4.1053
6.6594
112.23
25.7
L3
4.1053
6.6643
112.32
22.8
L4
4.1053
6.6615
112.27
27.9Here, a decrease in the “c” parameter values, as well as in the cell volume, is observed in the sample immersed during 45 min. With the increase of immersion time up to 60 and 75 min, both parameters increase slightly, stabilizing the crystal cell. Finally, at 90 min, a decrease of these parameters due to the shrinkage of the cell is observed, in agreement with Vegard’s law.Raman analysis of the different films was performed to evaluate the immersion time effect on the lattice vibrations of the CdS compound. According to the literature, the cadmium sulfide possesses a space group P63mc(C46v) with four atoms per unit cell. Hence, nine vibrations can be predicted at the zone-center optical phonon modes as follows: 2A1 + 1A2 + 1B1 + 1B2 + 2E1 + 2E2, where six modes at the zone center 2A1 + 2E1 + 2E2 are active in the Raman spectra [28, 29].Figure2 shows the deconvolution of the Raman spectrum for the CdS reference film, where two dominant optical vibrational modes located at 300 and 600 cm−1, approximately, are observed. These signals can be assigned to the fundamental longitudinal optical phonon mode E1(LO) and its first overtone mode (2LO), respectively [28, 29]. Similar behavior has been observed in different II-VI family compounds studied under resonant conditions, which could explain the dominance of the LO mode and its overtone in the spectra [30, 31]. Additionally, to improve the experimental data fitting, the spectrum in the regions around the LO and 2LO peaks was deconvoluted through several additional Lorentzian functions using the Fityk software™ [32]. The results revealed considerable asymmetry on the low and high frequency side in both optical modes (LO and 2LO). The identified principal vibrations modes as well as FWHM from this fitting are summarized in Table 2, which correspond mainly to a transversal optical (TO) and multiphonon modes [29, 33, 34]. Similar approach as the one developed in the deconvolution of the reference sample spectrum has been used to fit the set of remaining Raman spectra (L1, L2, L3, and L4).Figure 2
Deconvolution of the Raman spectra for the CdS reference film (L0).Table 2
Summary of centers and FWHM (in parentheses) for the different optical vibrational modes observed in all set Raman spectra.
Sample
Fundamental optical phonon
First overtone
E
1(TO)
E
2(SO)
E
1(LO)
E
2 (m)
E
2 (m)
E
2 (m)
2E1(LO)
2E2 (m)
2E2 (m)
L0
231.9 (48.4)
255.0 (43.2)
300.0 (29.8)
344.0 (31.6)
375.4 (21.3)
559.1 (36.2)
598.1 (41.0)
629.5 (41.6)
676.1 (40.0)
L1
234.1 (34.8)
257.0 (34.5)
301.0 (28.1)
344.7 (26.8)
377.0 (26.9)
559.3 (34.7)
598.7 (35.2)
609.8 (38.6)
661.2 (45.4)
L2
235.4 (37.2)
258.2 (33.8)
300.7 (26.2)
343.9 (38.0)
379.9 (28.5)
557.6 (35.3)
599.8 (41.0)
635.6 (41.2)
675.7 (36.4)
L3
238.6 (44.3)
255.6 (25.5)
300.5 (25.6)
341.2 (35.3)
376.0 (25.6)
558.6 (37.8)
599.4 (39.1)
631.8 (35.4)
665.4 (34.4)
L4
235.8 (33.0)
253.6 (43.2)
301.0 (29.5)
344.4 (31.9)
377.2 (26.3)
562.2 (30.6)
598.7 (39.4)
630.4 (41.8)
672.6 (34.2)Figure3 shows the set of Raman spectra of the different samples for their comparison. Each of these spectra was deconvoluted in nine Lorentzian line shape signals, which are observed at 235, 255, 300, 344, 370, 560, 598, 630, and 680 cm−1 approximately. Here, in all the spectra, a similar behavior can be detected, also that the LO and 2LO optical modes do not undergo any significant shift with the immersion time, maintaining their position near to 300 and 598 cm−1, respectively (Table 2). The corresponding positions for the different optical vibrational modes observed in the complete set of samples and the results are collected in Table 2. According to the literature, the optical vibrations located at ≈235 and 252 cm−1 can be classified as doubly degenerate E1(TO), while vibration observed at ≈254 cm−1 is commonly assigned either to surface optical (SO) or zone-edge (ZE) phonons (mainly in studies concerned with free-standing nanoparticles).Figure 3
Raman spectra set obtained for the CdS : Cu films obtained by ionic exchange process in aqueous solution.On the contrary, Raman bands located at 344, 377, and 560 cm−1 are the results from the active participation of the multiphonon scattering processes E2(m) or some combination these modes. In this sense, the asymmetry in the high frequency side of the LO optical mode can be denoted as HFS (high-frequency shoulder) which assumes the combination of the Raman signals located at 344 and 377 cm−1, respectively, as proposed in the earlier literature [31, 35, 36]. Similarly, the low-frequency asymmetry of the 2LO mode (344 cm−1) can be assigned to combination of (LO + E2) and/or (LO + E1/TO) modes, and similar assignments have been found in the literature for the SO mode, derived from the sum of frequency and shape [36].The modes located at 630 and 680 cm−1 around the 2LO peak have been assigned similarly to the HFS of the LO one (combination of multiphonon processes) [36]. Finally, from Raman analysis it can be noted that both low- and high-frequency asymmetry correlates with the density of phononic states and therefore can be related with phonon modes (or their combinations) activated by surface of the grains, with the latter playing the role of disorder for bulk-like phonons as described by Han and Bester [37].Note that in Figure3, any feature related with the formation of copper sulfide phase during the immersion of the CdS films in the cationic solution are not displayed, since the vibrational modes corresponding to the S-S bonds (intense peak at 465 cm−1) are not displayed, and this evidence confirms that any copper sulfide phase was formed during the immersion of the CdS films in the cationic solution (or its amount is below the detection limit) [38–40].


### 3.2. Morphological and Compositional Properties

Figure4 shows the SEM micrographs of some samples, including the CdS film reference. Figure 4(a) corresponds to the CdS reference. It can be observed that this sample presents a homogeneous distribution of particles with a compact and uniform appearance.Figure 4
SEM images of CdS thin films placed into CuCl2 solution at different immersion times (a) CdS reference, (b) 60 min, (c) 75 min, and (d) 90 min.
(a)
(b)
(c)
(d)In Figures4(b)–4(d), a clear change in the surface morphology is observed in the samples immersed during 60, 75, and 90 min, respectively. In these micrographs, an increase in the particle size as well as nonuniform agglomerates at perpendicular direction to substrate is observed. At 60 min, it was detected that the immersion into the CuCl2 solution promotes a change in the particle size, yielding a change in the surface morphology of the sample. Also, at larger immersion times, the formation of nonuniform agglomerates is observed, promoting a rougher and less smooth surface. Similar morphologies have been observed in CuxS thin films obtained by chemical bath deposition, in particular our research group has reported similar morphologies in CuxS thin films obtained by ammonia-free process [41].Hence, these changes might be associated directly to the Cu2+ atoms substitution (disorder effect), promoting mainly surface changes due to the deformation of the CdS crystalline lattice [27, 42]. In this sense, the major amount of Cu2+ atoms will be distributed homogeneously over CdS film surface, despite this, the formation of CuxS compound was not promoted as demonstrated by X-ray diffraction and Raman spectroscopy.WDS measurements were carried out by a “thick film analysis” to obtain quantitative information about the chemical composition of the different CdS-Cu films. Figure 5 shows an average concentration plot for the L0, L2, L3, and L4 samples. Note that the CdS film reference presents a Cd : S ratio equal to 1. The L2 sample immersed during 45 min into CuCl2 solution shows a decrease of 3% in the Cd atoms, and the quantity which was replaced by Cu atoms maintained a similar proportion of S atoms (∼50%) with respect to the reference. Additionally, a larger variability in the composition of this sample in comparison with the L3 and L4 samples can be seen indicating an aleatory substitution of the Cu2+ atoms within crystal host lattice. As the immersion time increases, this composition variability is reduced, and more cadmium atoms are replaced by copper atoms yielding a final composition of Cd0.95Cu0.05S approximately (90 min). That is, about 10% of Cd atoms were substituted during the longest immersion process. Nevertheless, some vacancies of S2− can be generated during the immersion process, and this explains the variability observed in the mean plot for the sulfur atoms.Figure 5
Elemental composition of CdS : Cu films obtained by ionic exchange process in aqueous solution.Therefore, based on the XRD patterns, Raman spectra, and WDS analysis, we suggest a scheme of the distribution of the Cu2+ atoms over the (002) planes in the CdS hexagonal structure as shown in Figure 6. Here, initially Cu atoms are distributed aleatory over the cadmium sulfide film surface deforming the crystalline structure (Figure 4(b)), subsequently, a larger quantity of cations is introduced into crystalline lattice stabilizing the crystal lattice again. Finally, at the longest immersion time, ten percent of the Cd atoms are substituted by Cu atoms inducing a decrease in the lattice parameters due to the shrinkage of the cell.Figure 6
Schematic distribution of the Cu2+ atoms over the (002) plane within crystalline structure of CdS.


## 3.1. Structural Properties

The CdS thin films obtained in this work presented uniform distribution on the substrate (observed by the eye), specular with light-yellow appearance and, also showed good adherence to the substrate. After immersion in the cationic solution, with the increase of the immersion time, the CdS films changed their appearance from yellowish to greenish color. This color change can be interpreted as the first evidence of the incorporation of copper atoms within crystalline structure of the cadmium sulfide. That is, Cu2+ ions can be incorporated into CdS thin films substituting Cd2+ by means of simple ion exchange process in aqueous solution, according to the following equation:(1)CdS+CuCl2⟶CuS+CdCl2where, the cations ligated within their crystal host lattice can be substituted with those present in the solution.Figure1 shows the X-ray patterns obtained for the different samples, here is included the CdS reference film labeled as L0. As observed, all the patterns show an intense diffraction peak at 2θ ≈ 26.7°, which could correspond to the (002) reflection of the CdS hexagonal phase or the (111) reflection of the CdS cubic structure. The predominance of this reflection in the XRD patterns indicates that the films are polycrystalline with high preferential orientation along the (002) or (111) crystalline direction. As well, the pattern of the CdS films show reflections located at 2θ ≈ 44 and 53° that can be assigned to the (220) and (331) crystalline planes of the cubic phase (JCPS #01-010-0454) or (110) and (112) planes of the hexagonal structure (JCPS #01-080-0006) of CdS, respectively. However, a reflection located at 2θ ≈ 48°, which explicitly corresponds to the (103) reflection of the hexagonal phase of CdS is also detected. Presence of this last reflection might suggest that the precursor solution used in this work favors the formation of a predominantly hexagonal phase. Similar outcomes have been reported by several research groups in CdS thin films obtained by chemical bath deposition in basic medium [22–24]. On the contrary, note that, in the XRD patterns for the samples L1, L2, L3, and L4, neither CuS nor Cu2S diffraction maxima are observed, indicating that these phases were not formed during the immersion process.Figure 1
XRD patterns set for CdS : Cu films obtained by ionic exchange process in aqueous solution. The inset in the upper-right zone is an enlargement around the (002) reflection.From the XRD analysis, we can observe two important effects in the principal (002) reflection as immersion time of the sample within the cationic solution increases: (i) it is slightly shifted to larger values of 2-theta and (ii) its intensity decreases. This can be explained as follows: the copper atoms present in the cationic solution can replace the Cd atoms ligated within the crystal lattice of the CdS, producing substitutional doping [25]. The observed structural changes originate from the difference between the ionic radius of both cations (Cu2+ = 87 pm and Cd2+ = 109 pm). According to Bragg’s law, the slight shift of the (002) diffraction peak towards larger values of 2-theta is related with the shrinkage of the c lattice constant of the hexagonal cell, which can be explained by the substitution of Cd cations by smaller Cu ones in the CdS crystalline lattice. On the contrary, the substitution of the Cd atoms by Cu atoms promotes disorder into the crystalline host cell; consequently, the width and intensity of the (002) peak is affected directly by the order-disorder effect [26, 27]. These phenomena can be explained as follows: when the CdS films are immersed into the cationic solution, the Cd atoms are displaced from the crystalline host cell destabilizing their structure (disorder effect); subsequently, the vacancy sites are occupied by Cu atoms stabilizing the crystal lattice again (order effect).The latter effect can be better observed in the inset of Figure1, where a meaningful decrease in the (002) reflection intensity is observed during the first 45 min immersion; afterward at 60 and 75 min, the (002) reflection intensity increases slightly, due to the reorder of the atoms as mentioned before. At 90 min, a decrease is observed again owing to direct substitution of Cd atoms by Cu atoms (Cu radius < Cd radius). This situation can be validated through the difference observed in the crystalline parameters of the CdS : Cu films, determined from XRD patterns, using the Jade 9.7 software™ (Table 1).Table 1
Cell parameters of CdS : Cu thin films obtained by XRD.
Sample
a (Å)
c (Å)
Cell volume (Å3)
Crystallite size (nm)
L0
4.1053
6.6802
112.58
26.2
L1
4.1053
6.6587
112.22
21.8
L2
4.1053
6.6594
112.23
25.7
L3
4.1053
6.6643
112.32
22.8
L4
4.1053
6.6615
112.27
27.9Here, a decrease in the “c” parameter values, as well as in the cell volume, is observed in the sample immersed during 45 min. With the increase of immersion time up to 60 and 75 min, both parameters increase slightly, stabilizing the crystal cell. Finally, at 90 min, a decrease of these parameters due to the shrinkage of the cell is observed, in agreement with Vegard’s law.Raman analysis of the different films was performed to evaluate the immersion time effect on the lattice vibrations of the CdS compound. According to the literature, the cadmium sulfide possesses a space group P63mc(C46v) with four atoms per unit cell. Hence, nine vibrations can be predicted at the zone-center optical phonon modes as follows: 2A1 + 1A2 + 1B1 + 1B2 + 2E1 + 2E2, where six modes at the zone center 2A1 + 2E1 + 2E2 are active in the Raman spectra [28, 29].Figure2 shows the deconvolution of the Raman spectrum for the CdS reference film, where two dominant optical vibrational modes located at 300 and 600 cm−1, approximately, are observed. These signals can be assigned to the fundamental longitudinal optical phonon mode E1(LO) and its first overtone mode (2LO), respectively [28, 29]. Similar behavior has been observed in different II-VI family compounds studied under resonant conditions, which could explain the dominance of the LO mode and its overtone in the spectra [30, 31]. Additionally, to improve the experimental data fitting, the spectrum in the regions around the LO and 2LO peaks was deconvoluted through several additional Lorentzian functions using the Fityk software™ [32]. The results revealed considerable asymmetry on the low and high frequency side in both optical modes (LO and 2LO). The identified principal vibrations modes as well as FWHM from this fitting are summarized in Table 2, which correspond mainly to a transversal optical (TO) and multiphonon modes [29, 33, 34]. Similar approach as the one developed in the deconvolution of the reference sample spectrum has been used to fit the set of remaining Raman spectra (L1, L2, L3, and L4).Figure 2
Deconvolution of the Raman spectra for the CdS reference film (L0).Table 2
Summary of centers and FWHM (in parentheses) for the different optical vibrational modes observed in all set Raman spectra.
Sample
Fundamental optical phonon
First overtone
E
1(TO)
E
2(SO)
E
1(LO)
E
2 (m)
E
2 (m)
E
2 (m)
2E1(LO)
2E2 (m)
2E2 (m)
L0
231.9 (48.4)
255.0 (43.2)
300.0 (29.8)
344.0 (31.6)
375.4 (21.3)
559.1 (36.2)
598.1 (41.0)
629.5 (41.6)
676.1 (40.0)
L1
234.1 (34.8)
257.0 (34.5)
301.0 (28.1)
344.7 (26.8)
377.0 (26.9)
559.3 (34.7)
598.7 (35.2)
609.8 (38.6)
661.2 (45.4)
L2
235.4 (37.2)
258.2 (33.8)
300.7 (26.2)
343.9 (38.0)
379.9 (28.5)
557.6 (35.3)
599.8 (41.0)
635.6 (41.2)
675.7 (36.4)
L3
238.6 (44.3)
255.6 (25.5)
300.5 (25.6)
341.2 (35.3)
376.0 (25.6)
558.6 (37.8)
599.4 (39.1)
631.8 (35.4)
665.4 (34.4)
L4
235.8 (33.0)
253.6 (43.2)
301.0 (29.5)
344.4 (31.9)
377.2 (26.3)
562.2 (30.6)
598.7 (39.4)
630.4 (41.8)
672.6 (34.2)Figure3 shows the set of Raman spectra of the different samples for their comparison. Each of these spectra was deconvoluted in nine Lorentzian line shape signals, which are observed at 235, 255, 300, 344, 370, 560, 598, 630, and 680 cm−1 approximately. Here, in all the spectra, a similar behavior can be detected, also that the LO and 2LO optical modes do not undergo any significant shift with the immersion time, maintaining their position near to 300 and 598 cm−1, respectively (Table 2). The corresponding positions for the different optical vibrational modes observed in the complete set of samples and the results are collected in Table 2. According to the literature, the optical vibrations located at ≈235 and 252 cm−1 can be classified as doubly degenerate E1(TO), while vibration observed at ≈254 cm−1 is commonly assigned either to surface optical (SO) or zone-edge (ZE) phonons (mainly in studies concerned with free-standing nanoparticles).Figure 3
Raman spectra set obtained for the CdS : Cu films obtained by ionic exchange process in aqueous solution.On the contrary, Raman bands located at 344, 377, and 560 cm−1 are the results from the active participation of the multiphonon scattering processes E2(m) or some combination these modes. In this sense, the asymmetry in the high frequency side of the LO optical mode can be denoted as HFS (high-frequency shoulder) which assumes the combination of the Raman signals located at 344 and 377 cm−1, respectively, as proposed in the earlier literature [31, 35, 36]. Similarly, the low-frequency asymmetry of the 2LO mode (344 cm−1) can be assigned to combination of (LO + E2) and/or (LO + E1/TO) modes, and similar assignments have been found in the literature for the SO mode, derived from the sum of frequency and shape [36].The modes located at 630 and 680 cm−1 around the 2LO peak have been assigned similarly to the HFS of the LO one (combination of multiphonon processes) [36]. Finally, from Raman analysis it can be noted that both low- and high-frequency asymmetry correlates with the density of phononic states and therefore can be related with phonon modes (or their combinations) activated by surface of the grains, with the latter playing the role of disorder for bulk-like phonons as described by Han and Bester [37].Note that in Figure3, any feature related with the formation of copper sulfide phase during the immersion of the CdS films in the cationic solution are not displayed, since the vibrational modes corresponding to the S-S bonds (intense peak at 465 cm−1) are not displayed, and this evidence confirms that any copper sulfide phase was formed during the immersion of the CdS films in the cationic solution (or its amount is below the detection limit) [38–40].


## 3.2. Morphological and Compositional Properties

Figure4 shows the SEM micrographs of some samples, including the CdS film reference. Figure 4(a) corresponds to the CdS reference. It can be observed that this sample presents a homogeneous distribution of particles with a compact and uniform appearance.Figure 4
SEM images of CdS thin films placed into CuCl2 solution at different immersion times (a) CdS reference, (b) 60 min, (c) 75 min, and (d) 90 min.
(a)
(b)
(c)
(d)In Figures4(b)–4(d), a clear change in the surface morphology is observed in the samples immersed during 60, 75, and 90 min, respectively. In these micrographs, an increase in the particle size as well as nonuniform agglomerates at perpendicular direction to substrate is observed. At 60 min, it was detected that the immersion into the CuCl2 solution promotes a change in the particle size, yielding a change in the surface morphology of the sample. Also, at larger immersion times, the formation of nonuniform agglomerates is observed, promoting a rougher and less smooth surface. Similar morphologies have been observed in CuxS thin films obtained by chemical bath deposition, in particular our research group has reported similar morphologies in CuxS thin films obtained by ammonia-free process [41].Hence, these changes might be associated directly to the Cu2+ atoms substitution (disorder effect), promoting mainly surface changes due to the deformation of the CdS crystalline lattice [27, 42]. In this sense, the major amount of Cu2+ atoms will be distributed homogeneously over CdS film surface, despite this, the formation of CuxS compound was not promoted as demonstrated by X-ray diffraction and Raman spectroscopy.WDS measurements were carried out by a “thick film analysis” to obtain quantitative information about the chemical composition of the different CdS-Cu films. Figure 5 shows an average concentration plot for the L0, L2, L3, and L4 samples. Note that the CdS film reference presents a Cd : S ratio equal to 1. The L2 sample immersed during 45 min into CuCl2 solution shows a decrease of 3% in the Cd atoms, and the quantity which was replaced by Cu atoms maintained a similar proportion of S atoms (∼50%) with respect to the reference. Additionally, a larger variability in the composition of this sample in comparison with the L3 and L4 samples can be seen indicating an aleatory substitution of the Cu2+ atoms within crystal host lattice. As the immersion time increases, this composition variability is reduced, and more cadmium atoms are replaced by copper atoms yielding a final composition of Cd0.95Cu0.05S approximately (90 min). That is, about 10% of Cd atoms were substituted during the longest immersion process. Nevertheless, some vacancies of S2− can be generated during the immersion process, and this explains the variability observed in the mean plot for the sulfur atoms.Figure 5
Elemental composition of CdS : Cu films obtained by ionic exchange process in aqueous solution.Therefore, based on the XRD patterns, Raman spectra, and WDS analysis, we suggest a scheme of the distribution of the Cu2+ atoms over the (002) planes in the CdS hexagonal structure as shown in Figure 6. Here, initially Cu atoms are distributed aleatory over the cadmium sulfide film surface deforming the crystalline structure (Figure 4(b)), subsequently, a larger quantity of cations is introduced into crystalline lattice stabilizing the crystal lattice again. Finally, at the longest immersion time, ten percent of the Cd atoms are substituted by Cu atoms inducing a decrease in the lattice parameters due to the shrinkage of the cell.Figure 6
Schematic distribution of the Cu2+ atoms over the (002) plane within crystalline structure of CdS.


## 4. Summary and Conclusions

We have described a possible mechanism for the incorporation of copper atoms into the structure of CdS thin films by a simple ion exchange process, using an ammonium-free chemical bath deposit process and a subsequent immersion in a CuCl2 solution at 45, 60, 75, and 90 min, to achieve the ion exchange, generating CdxCu1-xS films. A first indicative of the change in the chemical composition was followed by the change in color from yellowish to greenish.The X-ray analysis suggested that the CdS films developed a hexagonal structure, with preferential orientation along the plane (002), corroborated by the presence of one reflection located at 2θ ≈ 48°, which explicitly corresponds to the (103) reflection of the hexagonal phase of CdS. During the ion exchange, a decrease in the intensity of the reflection (002) was observed as well as a slight displacement of this reflection towards higher values of 2θ derived from the substitution of Cd atoms by Cu atoms. The WDS analysis revealed that approximately 10% of the cadmium atoms were replaced by copper atoms after 90 min of immersion.



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*Source: 1095204-2018-08-01.xml*