Synthesis and Characterization of Colloidal CZTS Nanocrystals by a Hot-Injection Method

Méndez-López, A.; Morales-Acevedo, A.; Acosta-Silva, Y. J.; Ortega-López, M.

doi:https://doi.org/10.1155/2016/7486094

Journal of Nanomaterials

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Abstract Introduction Experimental Results and Discussion Conclusions Acknowledgments References Copyright Related Articles

Research Article | Open Access

Volume 2016 | Article ID 7486094 | https://doi.org/10.1155/2016/7486094

Synthesis and Characterization of Colloidal CZTS Nanocrystals by a Hot-Injection Method

A. Méndez-López,^1,2A. Morales-Acevedo,¹Y. J. Acosta-Silva,³and M. Ortega-López¹

Academic Editor: Mohamed Bououdina

Received28 Jan 2015

Revised02 Jun 2015

Accepted11 Nov 2015

Published14 Apr 2016

Abstract

The present study reports the synthesis of colloidal Cu₂ZnSnS₄ (CZTS) nanocrystals (average size ~4–9 nm) by a simple and low cost hot-injection method. These nanocrystals form larger particles with sizes around 40 nm. Oleylamine (OLA) was used as both the solvent and the nanocrystal stabilizer. The effect of the synthesis time on the structural, compositional, morphological, and optical properties was studied. As revealed by XRD, Raman, and TEM measurements all the prepared samples are comprised of both kesterite and wurtzite CZTS nanocrystals. The wurtzite phase contribution reduces as the reaction time is increased. The “bandgap” of the obtained nanoparticles tends to 1.52 eV for the larger synthesis times (24 h) which is suitable for an absorber layer in thin films solar cells.

1. Introduction

The Cu₂ZnSnS₄ (CZTS) is a direct band gap semiconductor with high absorption coefficient in the visible region (>10⁴ cm⁻¹) and an energy band gap in the 1.4–1.6 eV range, which is very close to the optimum value for the absorber layer of thin film solar cells [1, 2]. In the last years CZTS has intensively been studied as a promising cheap and green photovoltaic material, because it comprises earth abundant and nontoxic elements [3]. To date, CZTS thin films have been prepared by various experimental techniques such as atom beam sputtering [4], thermal evaporation of its constituents [5], spray pyrolysis [6], and sol-gel [7]. Recently, colloidal CZTS nanocrystals prepared by the hot-injection method have paid much attention in the solution processable solar cells technology, because its chemistry and viscosity can be tailored to be used as the raw material in the thin films deposition using ink-printing, spraying, dip-coating, or roll-to-roll coating under ambient condition [8]. CZTS displays polymorphism with kesterite or stannite crystal structure. At the nanometer scale, CZTS also crystallizes in the kesterite or stannite phase, which resemble the tetragonal unitary cell [9, 10]. Recently, however, several workers reported the synthesis of colloidal wurtzite CZTS by hot-injection method [11, 12]. In this contribution, we present the synthesis and characterization of colloidal CZTS nanocrystals with the kesterite as the predominant phase. The nanocrystals are readily produced by using thioacetamide as the sulfur source in oleylamine. The structural and optical properties of colloidal nanocrystals formation have been systematically studied by X-ray diffraction, Raman spectroscopy, scanning electron microscopy (SEM), energy dispersive X-ray spectroscopy (EDS), transmission electron microscopy (TEM), and UV-Vis.

2. Experimental

2.1. Synthesis of CZTS Nanocrystals

Colloidal CZTS nanocrystals were synthesized by hot-injection using oleylamine as solvent and capping agent, following a procedure first reported by Joo et al. [13] with slight modifications. In a typical synthesis of CZTS nanocrystals, 2 mmol of copper (II) chloride dihydrate (CuCl₂, 99%, Aldrich), 1 mmol of zinc chloride (ZnCl, 99%, Aldrich), 1 mmol of Tin (II) chloride dihydrate (SnCl₂, 98%, Aldrich), and 20 mL of oleylamine (OLA, 70%, Fluka) were mixed in a 50 mL three-neck round-bottom flask, stirred and heated to 170°C for 1 h under inert atmosphere of argon (99.999%). When the temperature reached 120°C, the color of the mixture gradually changed from dark blue to a brown-yellow color. Meanwhile, another solution was prepared, for which 4 mmol thioacetamide was dissolved in 3 mL oleylamine, under magnetic stirring, until the thioacetamide was dissolved and a green-yellow solution was obtained. Afterwards, brown-yellow solution was heated to 230°C and the thioacetamide-oleylamine solution was rapidly injected; then the temperature mixture solution was kept during different times, 3–24 hours. After the reaction had finished, the flask was removed from the heating mantle and allowed to naturally cool to room temperature; 5 mL of toluene was added to the flask. To washing or purifying the product, 40 mL of ethanol was firstly added and went through ultrasonic dispersion for 30 min and was then centrifuged at 4000 rpm for 30 min to let the nanocrystals flocculate and precipitate to remove some unreacted chemicals and byproducts; its precipitate was redispersed by adding 40 mL of ethanol ultrasonically for 30 min and nanocrystals were again isolated by centrifugation at 4400 rpm for 30 min, with the purpose of letting the nanocrystals flocculate and precipitate to again remove some unreacted chemicals and byproducts. The above process was repeated for three times. The final precipitates (or CZTS nanocrystals) were dispersed in ethanol to form a stable ink solution with high purity. CZTS films were prepared on a soda-lime glass by drop-coating, drying at room temperature.

2.2. Characterization Methods

The crystallographic information of the nanocrystals was obtained from the powder X-ray diffraction patterns (PANalytical X’pert PRO X-ray diffractometer), using the CuKα radiation with a wavelength of 1.5405 Å in the range 20–70°. Raman spectroscopy was carried out using a Jobin Horiba model microspectrometer, with a He-Ne laser that emitted a wavelength of 632.8 nm and a power of 20 mW. The Raman spectra samples were measured at room temperature in a wavelength range between 200 and 600 nm, using a 50x objective to focalize the laser spot. All spectra were calibrated with respect to the silicon Raman mode at 520.7 cm⁻¹. The morphology of CZTS nanocrystals was determined using an Auriga Zeiss 90-36 scanning electron microscope. Transmission electron microscopy study was obtained using a JEOL model 2010 transmission electron microscope, operating at 200 kV, with a point to point resolution of 0.18 nm.

3. Results and Discussion

3.1. XRD Characterization

As above explained, CZTS nanocrystals were synthesized by a hot-injection method in which the thioacetamide precursor was poured into a hot solution at a given reaction temperature.

In order to gain insight on the nanocrystals formation process, we examined the nanocrystals synthesized at 230°C and the synthesis time was varied from 3 h to 24 h.

Figure 1 shows the XRD patterns of the CZTS nanocrystals synthesized. The XRD pattern of CZTS nanocrystals synthesized at 3 hours displays no discernible peaks, indicating a sample containing amorphous or very small particles. For reaction times of 6 h and longer, a series of the XRD peaks were observed. All well crystallized samples appear to consist of nanocrystals in which the kesterite and wurtzite phases coexist. The wurtzite planes were indexed according to simulated wurtzite patterns All the diffraction peaks appearing at 2θ = 27.282°, 28.365°, 30.829°, 39.829°, 48.244°, 51.792°, 56.161°, 56.908°, and 58.639° can be attributed to the (100), (002), (101), (102), (110), (103), (200), (112), and (201) planes of the wurtzite structure of CZTS [14]. There are some additional diffraction peaks at 2θ = 28.365°, 32.983°, 47.248°, and 56.161°. These peaks can be attributed to the (112), (200), (220), and (312) planes of the kesterite structure of CZTS. There is great similarity in the position of some peaks in the two crystal structures (wurtzite and kesterite). The weak diffraction peak at around 33°, which corresponds to the (200) plane of kesterite CZTS, can be used to track the kesterite crystal phase during the formation of the CZTS nanocrystals in the samples. Notice that the positions of the peaks associated with the (002) plane of the wurtzite coincide with the (112) peak associated with the kesterite structure. In addition, the diffraction due to the (200) planes of wurtzite coincides with the (312) planes for the kesterite phase. Then, we can conclude that there is a mixture of both kesterite and wurtzite phases of the CZTS nanocrystals in the films, but we cannot determine the relative fractions for each phase in our samples. The lattice parameters determined from the observed (002) and (101) spacing of the crystallites with the wurtzite structure were = 3.7637 Å and = 6.2259 Å, in good agreement with the reported single crystal data of = 3.81 Å and = 6.28 Å [15]. For the crystallites with the kesterite structure, the lattice parameters are = 5.43 Å and = 10.92 Å, as determined from the spacing of the (200) and (112) planes which are very similar to those reported for kesterite CZTS powders (JCPDS 26-0575).

The average size of the nanoparticles can be estimated from the XRD data using Scherrer’s equation [16]:where represents the crystallite size (nm), = 1.5406 Å is the X-ray wavelength (for CuKα line), is the peak width at half-maximum (FWHM, units in radians), is the angle of reflection, and = 0.9 is the shape factor. In accordance with the above, we can observe that the CZTS particle sizes increase for longer reaction times during the synthesis. The particle sizes on these films were estimated to be ~20 to ~40 nm.

3.2. Raman Spectroscopy Analysis

We used Raman spectroscopy to verify that all samples were pure CZTS without secondary phases. Indeed, Raman spectroscopy is a valuable tool to clearly identify CZTS and the binary (ZnS, , SnS₂) or ternary (Cu₃SnS₄) chalcogenides which could originate during the CZTS synthesis. The main Raman peak for these chalcogenides comes out at 351 cm⁻¹ (ZnS), 475 cm⁻¹ (), 315 cm⁻¹ (SnS₂), and 348 cm⁻¹ (Cu₃SnS₄). Kesterite CZTS, on the other hand, displays Raman peaks at 252, 287, 339, 351, and 368 cm⁻¹, with the highest intensity at 339 cm⁻¹ [17]. Raman peaks for the wurtzite type structure of CZTS are reported in the range 331–338 [18].

Figure 2 shows the Raman spectra of the CTZS samples prepared at different reaction times. The Raman peak at 339 cm⁻¹ (ascribed to vibrational A1 mode of kesterite CZTS) suggests that the kesterite phase predominates in our CZTS samples. This Raman peak shifted to lower wave numbers, particularly for short synthesis times, implies that the wurtzite phase is present, but it diminishes as the deposition time is increased. The Raman spectra for the samples synthesized during large times (24 hours) are more typical of kesterite CZTS, but the peaks are broader with respect to those already reported, probably due to the small particle size effects. However, notice that the short range order of the CZTS nanocrystals forming the nanoparticles increases as the deposition time is increased. For the nanocrystals synthesized during 3 hours, the Raman peak intensity is very low, indicating that the CZTS particle size is very small, which is consistent with the XRD results.

3.3. Scanning Electron Microscopy (SEM)

The chemical composition of our samples was assessed by scanning electron microscopy-energy-dispersive X-ray spectroscopy (SEM-EDX). For simplicity, only the metals (Cu, Zn, and Sn) were considered. This restriction is reasonable because there is always an excess of sulphur (S) during preparation, and it introduces only a small error in the film composition because the S contents were always close to 50%. The stoichiometric composition of CZTS should be 2 : 1 : 1 : 4. We can see clearly in Table 1 that as the synthesis time is increased we are having a composition which tends more to this CZTS stoichiometry. Short synthesis times cause low zinc content in the samples. Zaberca et al. obtained a similar result using isopropanol as the solvent by a polycondensation reaction at 200°C [19]. Woo et al. reported results obtained with Cu-poor and Zn-rich compositions [17], and Chen et al. mentioned that for improved efficiency of solar cells CZTS must have a Cu-poor and Zn-rich composition, as the Zn atoms in excess enter into the Cu vacancies [20]. Our synthesis process for 15 hours meets these characteristics. The results for 18, 21, and 24 hours are very similar, with compositions which are close to the volumetric CZTS stoichiometry.

Figure 3 shows the surface SEM image of Cu₂ZnSnS₄ nanocrystals dip-coated onto the SLG substrate. In Figure 3(a), it can be seen that reaction times of 3 h cause smoother surfaces and compact films than for larger times. Previous works report similar result with Cu-poor/Zn-rich composition [21].

For low synthesis times the SEM images show that the clusters were nonuniformly distributed over the substrate surface. However, the surface morphology of the 24 h sample (Figure 3(f)) shows that this sample has a uniform granular morphology with good homogeneity during the nanoparticle growth.

3.4. Transmission Electron Microscopy (TEM)

A representative transmission electron microscopy (TEM) image of the CZTS nanocrystals produced for 24 hours is shown in Figure 4(a). The CZTS nanocrystals are slightly irregular and polydisperse. Homogeneous size control is still not available by this method for such complex quaternary materials. A high-resolution TEM image of a few selected particles (Figure 4(b)) shows that the CZTS nanocrystals produce clear lattice fringes. The fringes are regular with spacings = 0.33 nm and = 0.31 nm, which corresponds to the (100) lattice plane, and to the (002) lattice plane of wurtzite CZTS nanocrystals, respectively. In the inset of Figure 4(c), we plot a distribution of particle sizes as extracted from the TEM image. The sizes of the nanocrystals are found in the range from 4 nm to 9 nm. We find that these values are not the same as determined from the XRD data because XRD peaks are associated with clusters (nanoparticles) formed by the CZTS nanocrystals. From the selected area electron diffraction (SAED) pattern, tetragonal symmetry was confirmed. The spots in the SAED pattern could very well be indexed to the planes observed by XRD (Figure 4(d)). Furthermore, the lattice spacing observed in these HR-TEM images of 3.3 Å and 3.1 Å corresponds to the (100) and (002)/(112) planes of CZTS, respectively. Then we confirm the tetragonal symmetry for the prepared CZTS nanocrystals (Figure 4(c)).

3.5. UV-Vis Absorption Spectra

The semiconducting band gap has been estimated based on its optical absorption properties investigated by UV-Vis absorption spectroscopy. As being a direct band gap semiconductor of CZTS, its band gap can be obtained from the versus , where is the quantum energy of incident photons, and is the absorption coefficient (Abs). The absorption curve and the derived curve of versus are shown in Figure 5(a) for the sample synthetized during 3 hours and in Figure 5(b) for the other samples at longer times.

(a)

(b)

The band gap is determined from the Tauc plots [22]:where is a constant, is incident photon frequency, is Planck’s constant, and is the band gap energy. The band gap energy is obtained by extrapolating the tangent line of the curve to the -axis. The linear nature of the graphs supports the direct band gap nature of the semiconductor. The obtained values are 1.75, 1.71, 1.61, 1.59, 1.56, and 1.52 eV, respectively, which is in good agreement with CZTS band gap values reported by other authors [23–26]. As can be seen from Figure 5(a), for the 3 h samples two absorbing edges appear indicating two band gaps of 1.75 eV and 2.08 eV, respectively, as shown in the inset. This indicates that there is not a single phase for these films. The possible secondary phases cannot be detected from either XRD or Raman spectra, due to its possible amorphous character and small particle sizes observed for the 3 hours samples. For larger synthesis times the observed results tend to the optical band gap of 1.52 eV, which is suitable for an absorber layer in thin films solar cells (Figure 5(b)).

4. Conclusions

In this contribution, we have shown that the quaternary semiconductor compound CZTS can be synthesized by a hot-injection method at constant temperature for 3–24 hours. The obtained nanoparticles are formed by a mixture of both kesterite and wurtzite nanocrystals. The structures were studied by TEM, energy dispersive X-ray spectroscopy, and XRD. The factors that influence the formation of the CZTS nanocrystals were investigated. We found that, for long reaction times, the zinc atoms become embedded in the compound for the formation of CZTS nanocrystals with a thermodynamically metastable kesterite/wurtzite mixture. The XRD profile reveals the formation of this CZTS crystalline phase mixture with a decreasing amount of the wurtzite phase as the synthesis time is increased. This fact was confirmed by Raman spectroscopy and TEM electron diffraction patterns. In addition, EDX-analysis of the samples showed that the chemical composition of the CZTS nanocrystals is near the stoichiometric value. The prepared nanocrystals exhibit diameters between 4 and 9 nm. This synthesized nanoparticles size estimated by XRD (Scherrer formula) is around 20–40 nm. The nanoparticles are formed by nanocrystallites with sizes around 4–9 nm as determined from TEM measurements. The “band gap” of the obtained particles tends to 1.52 eV for the larger synthesis times (24 h) which is suitable for an absorber layer in thin films solar cells. Our work provides a surfactant-free and solvent-redispersible hot-injection nanocrystal fabrication process which is simple, of low cost, and nontoxic.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.

Acknowledgments

A. Méndez-López thanks Mr. Alvaro Guzman for the synthesis of nanoparticles and also M. C. Adolfo Tavira (XRD) and M. C. Miguel Galvan (Raman Spectroscopy) for their technical assistance. A. Méndez-López gratefully thanks Doctors Yasuhiro Matsumoto and Genaro Martin Soto-Zarazua and Professor Hironori Katagiri for their help which improved this work significantly.

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Copyright © 2016 A. Méndez-López et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

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