- Nano Express
- Open Access
Influence of crystal structure of nanosized ZrO2 on photocatalytic degradation of methyl orange
© Basahel et al.; licensee Springer. 2015
- Received: 17 September 2014
- Accepted: 22 January 2015
- Published: 18 February 2015
Nanosized ZrO2 powders with near pure monoclinic, tetragonal, and cubic structures synthesized by various methods were used as catalysts for photocatalytic degradation of methyl orange. The structural and textural properties of the samples were analyzed by X-ray diffraction, Raman spectroscopy, TEM, UV-vis, X-ray photoelectron spectroscopy (XPS), and N2 adsorption measurements. The performance of synthesized ZrO2 nanoparticles in the photocatalytic degradation of methyl orange under UV light irradiation was evaluated. The photocatalytic activity of the pure monoclinic ZrO2 sample is higher than that of the tetragonal and cubic ZrO2 samples under optimum identical conditions. The characterization results revealed that monoclinic ZrO2 nanoparticles possessed high crystallinity and mesopores with diameter of 100 Å. The higher activity of the monoclinic ZrO2 sample for the photocatalytic degradation of methyl orange can be attributed to the combining effects of factors including the presence of small amount of oxygen-deficient zirconium oxide phase, high crystallinity, large pores, and high density of surface hydroxyl groups.
- Structural effect
- Photocatalytic degradationl
- Methyl orange
The rapid growth of the textile industry has led to the accumulation of various organic pollutants, with dyes accumulating in bodies of water as a particularly severe example. This type of aquatic pollution has indirect or direct adverse effects on the biosphere . Photocatalysis is one promising approach to protect the aquatic environment based on its ability to oxidize low concentrations of organic pollutants in water [2,3]. In the past two decades, many oxide and sulfide semiconductors such as TiO2, ZnO, WO3, SrTiO3, ZnS, and CdS were applied as photocatalysts for environmental control technology and also a wide range of chemical reactions . Recently, Kuriakose et al. [5,6], Cheng et al. , and Ren et al.  successfully employed ZnO- and TiO2-based nanomaterials for photocatalytic degradation of organic dyes. ZrO2 has been considered as a photocatalyst in different chemical reactions due to its relatively wide band gap value E g and the high negative value of the conduction band potential . The reported band gap energy of ZrO2 range was between 3.25 and 5.1 eV, depending on the preparation technique of the sample .
It is reported that a good manipulation of ZrO2 morphological tuning, porous structure control, and crystallinity development is required in order to enhance the light harvesting capability, prolong the lifetime of photoinduced electron-hole pairs, and facilitate the reactant accessibility to surface active sites . As ZrO2 is used in a wide variety of applications in addition to photocatalysis, the fabrication of identical ZrO2 nanoscale structures has been recently attracted a great deal of interest. Nanocrystalline ZrO2 with various attractive morphologies has been effectively prepared by different synthesis methods like hydrothermal synthesis, sol-gel synthesis, precipitation, and thermal decomposition .
It is well known that ZrO2 has three polymorphs : monoclinic, tetragonal, and cubic. Preparation methods play an important role in determining the final crystal structure of ZrO2. Although the different surface properties on different ZrO2 polymorphs have been extensively studied [14,15], the effect of crystal structures on photocatalysis has rarely been investigated.
Nawale et al.  synthesized ZrO2 samples using thermal plasma reactor at different operating pressures. The sample which contained both tetragonal and monoclinic phases synthesized at 1.33 bar of operating pressure showed the highest photocatalytic activity. The presence of tetragonal phase along with monoclinic phase indicates the crystallographic rearrangement in ZrO2 due to the oxygen vacancies. The authors related the photocatalytic properties of ZrO2 with the trap levels present in it due to oxygen vacancies. It was observed that the photocatalytic response tracks the energy gap of the monoclinic phase which varies with the varying synthesis parameters.
Zhao et al.  used anodization method to synthesize ZrO2 nanotubes with a length of 25 μm, inner diameter of 80 nm, and wall thickness of 35 nm. The authors observed 97.6 decolorization percentage of methyl orange in 8 h at optimal pH value 2. Ismail et al.  synthesized 6-μm-thick anodic oxide film with nanotubular ZrO2 structure, and the authors tested the photocatalytic ability of the ZrO2 nanotubes. The authors reported 30% of methyl orange degradation under UV light in the presence of the cubic/tetragonal ZrO2 nanotubes after 120 min of reaction.
Jiang et al.  used zirconium foil to anodize in electrolyte containing 1 M (NH4)2SO4 and 0.25 wt.% NH4F to in situ construct the ZrO2 nanotubes on the surface. The authors reported that ZrO2 nanotubes showed excellent photocatalytic performance with methyl orange photodegradation rate of 94.4% after 240 min. They also claimed that photocatalysis performance was due to the hydroxyl group absorbing on the surface.
Shu et al.  synthesized tetragonal star-like ZrO2 nanostructures using hydrothermal synthesis method. The authors used ZrO2 nanostructures for the photodegradation of anionic dyes including methyl orange, in acidic, neutral, and weak basic aqueous solutions. They observed that the ZrO2 sample offered complete degradation of methyl orange within 60 min; however, authors have not studied the stability and reusability of the synthesized ZrO2 nanomaterial.
The objective of the present study is to synthesize nanocrystalline mesoporous monoclinic, tetragonal, and cubic ZrO2 samples with high surface area using fairly simple experimental procedures. In this work, nanosized pure monoclinic, tetragonal, and cubic ZrO2 samples were prepared and the physico-chemical properties of the samples were performed by different characterization techniques. The photocatalytic degradation of methyl orange over the three ZrO2 samples were studied and correlated to the phase structure, specific surface area, and electronic properties of the catalysts.
Zirconyl chloride, zirconium isopropoxide, sodium hydroxide solution, methyl orange, and hydrochloric acid were purchased from Aldrich, Dorset, England, UK. All chemicals used in this study were analytical grade and used directly without further purification. Deionzied water was used for the preparation of the methyl orange standard solution as well as the respective dilutions.
Synthesis of pure monoclinic, tetragonal, and cubic ZrO2 samples
A near pure monoclinic nanocrystalline ZrO2 was synthesized by following the method reported by Guo et al. . The zirconyl chloride was dissolved in deionized water so that the final concentration of zirconium was 38.7 g per liter (0.42 M). Of the zirconyl chloride solution, 15 ml was added to 300 mL deionized water in a glass beaker, and then concentrated aqueous ammonia was added rapidly to the solution with constant stirring until pH 4.5. The resultant precipitate was aged in the mother liquor for 24 h. After filtration, it was washed several times with dilute ammonia and hot deionized water (80°C) until chloride ions were no longer detectable in the washing water (AgNO3 test) and then dried at 100°C for 12 h. The synthesized sample was calcined at 500°C for 3 h in air with a ramp rate of 1°C min−1 and kept isothermally for 3 h and was annotated as m-ZrO2.
Pure tetragonal ZrO2 was synthesized by the following reported procedure in the literature . Zirconium oxychloride and ammonia solution (25% w/w) solutions were prepared using deionized water. First, 50 mL of 2.5 M ammonia solution was added to 50 mL of 0.1 M zirconium oxychloride solution drop by drop in a beaker and the mixture was stirred vigorously at room temperature for 4 h. The white zirconium hydroxide precipitates in time of addition of ammonia solution. The obtained precipitate was separated by centrifugation at 4,000 rpm, washed with water and ethanol for several times. Then, the precipitate was transferred into Teflon-lined autoclave, and the autoclave was kept at 100°C for 12 h. Finally, the white powder was calcined in furnace at 500°C for 3 h with a ramp rate of 1°C min−1 and kept at this temperature for 3 h and was annotated as t-ZrO2.
Cubic ZrO2 was synthesized by hydrothermal method reported my Tahir et al. . In a Teflon vessel, 1 g of zirconium isopropoxide was dissolved in 6 mL of ethanol (99.8%) and then the Teflon vessel was kept in a desiccator containing a Petri dish filled with water at the bottom. The diffusion experiment was stopped after 12 h, followed by the addition of 25 mL of 10 M NaOH aqueous solution. Then, the reaction vessel was sealed into a stainless steel hydrothermal bomb, which was heated to 180°C for 18 h. After the autoclave was cooled down to room temperature, the products were filtered and repeatedly washed with 0.1 M HNO3, 1 N HCl, and deionized water. After drying under vacuum for 3 h, a white soft and fibrous powder was obtained. The obtained powder was calcined at 500°C for 3 h in air with a ramp rate of 1°C min−1 and kept isothermally for 3 h and was annotated as c-ZrO2.
where D is the average crystallite size of the phase under investigation, B is the Scherer constant (0.89), λ is the wavelength of the X-ray beam used (1.54056 A°), β 1/2 is the full width at half maximum (FWHM) of the diffraction peak, and θ is the diffraction angle. The identification of different crystalline phases in the samples was performed by comparing the data with the Joint Committee for Powder Diffraction Standards (JCPDS) files.
The Raman spectra of the samples were measured with a Bruker Equinox 55 FT-IR spectrometer equipped with an FRA106/S FT Raman module and a liquid N2-cooled Ge detector using the 1,064-nm line of a Nd:YAG laser with an output laser power of 200 mW.
A Philips CM200FEG microscope (Philips, Amsterdam, The Netherlands), 200 kV, equipped with a field emission gun was used for HRTEM analysis. The coefficient of spherical aberration was C s = 1.35 mm. The information limit was better than 0.18 nm. High-resolution images with a pixel size of 0.044 nm were taken with a CCD camera.
The textural properties of the prepared samples were determined from nitrogen adsorption/desorption isotherm measurements at −196°C using Autosorb automated gas sorption system (Quantachrome, Boynton Beach, FL, USA). Prior to measurement, each sample was degassed for 6 h at 150°C. The specific surface area, S BET, was calculated by applying the Brunauer-Emmett-Teller (BET) equation. The average pore radius was estimated from the relation 2V p/S BET, where V p is the total pore volume (at P/P0 = 0.975). Pore size distribution over the mesopore range was generated by the Barrett-Joyner-Halenda (BJH) analysis of the desorption branches, and the values for the average pore size were calculated.
The X-ray photoelectron spectroscopy (XPS) measurements were carried out by using a SPECS GmbH X-ray photoelectron spectrometer (SPECS, Berlin, Germany). Prior to analysis, the samples were degassed under vacuum inside the load lock for 16 h. The binding energy of the adventitious carbon (C 1 s) line at 284.6 eV was used for calibration, and the positions of other peaks were corrected according to the position of the C 1 s signal. For the measurements of high-resolution spectra, the analyzer was set to the large area lens mode with energy steps of 25 m eV and in fixed analyzer transmission (FAT) mode with pass energies of 34 eV and dwell times of 100 ms. The photoelectron spectra of the four samples were recorded with the acceptance area and angle of 5 mm in diameter and up to ±5°, respectively. The base pressure during all measurements was 5 × 10−9 mbar. A standard dual anode excitation source with Mg Kα (1,253.6 eV) radiation was used at 13 kV and 100 W.
The UV-vis absorption spectra in transmittance mode were recorded on a Thermo Scientific (Evolution 600 UV-vis; Thermo Fisher Scientific, Waltham, MA, USA) instrument. The optical bandgap of the samples is measured by plotting a (αhυ)2 versus hυ. The extrapolation of the straight line in the graph to (αhυ)2 = 0 gives the value of the energy band gap.
Photocatalytic degradation of methyl orange
where C o is the concentration of methyl orange before illumination and C is the concentration after a certain irradiation time.
X-ray powder diffraction
The percentages of monoclinic and oxygen deficient phases were found to be 97% and 3%, respectively, for the m-ZrO2 sample. There are no additional unindexed peaks in the m-ZrO2 sample.
XRD pattern of the t-ZrO2 sample showed peaks for pure tetragonal phase of ZrO2 [JCPDS 80-0965] at 2θ = 30.2°, 35.2°, 50.6°, and 60.2°. No additional peaks corresponding to any other phase was observed in XRD pattern of this sample. All of the diffraction peaks of the XRD pattern of the c-ZrO2 sample can be indexed to the standard pattern of the pure cubic phase of ZrO2. Peaks at 2θ = 30.3°, 35.14°, 50.48°, and 60.2° reveal the presence of (111), (200), (220), and (311) planes, respectively, of cubic ZrO2 according to JCPDS CAS number 27-0997. These observation indicates that the m-ZrO2 sample is near pure monoclinic; however, the t-ZrO2 and c-ZrO2 samples did not show presence of any additional phases or impurities indicating that these two phases are pure in composition. In addition, the intensities of diffraction peaks of the m-ZrO2 sample were much higher than those of the t-ZrO2 and c-ZrO2 samples indicating that the m-ZrO2 sample is highly crystalline than the t-ZrO2 and c-ZrO2 samples.
However, it is known that assignment of cubic and tetragonal structures, based solely on the X-ray diffraction analysis, can be misleading because the cubic and tetragonal structures (a 0 = 0.5124 nm for cubic and a 0 = 0.5094 nm and c 0 = 0.5177 nm for tetragonal structures) are very similar . The authors also reported that the tetragonal structure can be distinguished from the cubic structure by the presence of the characteristic splitting of the diffraction peaks, whereas the cubic phase exhibits only single peaks. A significant line broadening obscured any clear distinction between the tetragonal and cubic polymorphs of ZrO2 (Figure 1). However, this detection is possible by measuring with high step counting times the (112) Bragg reflection of the tetragonal structure, which is forbidden in the cubic symmetry . As it can be observed in Figure 1, a shift of the peak positions to higher 2θ values occurred. This shift may indicate a decrease in the lattice parameters.
The crystallite size was calculated using the Scherrer's equation (1). The average crystallite sizes of the monoclinic phase, calculated from the (111) diffraction peak was found to be 34 nm. Similarly, the average crystallite sizes, calculated from the (111) diffraction peak of the tetragonal and cubic phases, were found to be 17 and 20 nm for the t-ZrO2 and c-ZrO2 samples, respectively.
The Raman spectrum for c-ZrO2 is characterized by a narrow band at 145 cm−1 and broad bands centered at 246, 301, 436, and 625 cm−1. Gazzoli et al.  reported that the Raman peak at 149 cm−1 is common for both of tetragonal and cubic phases, and cubic ZrO2 presents the strong band between 607 and 617 cm−1. The c-ZrO2 sample in this study clearly showed the broad peak centered at 625 cm−1, and this sample also shows poorly defined features related to the disordered oxygen sub-lattice whereas tetragonal ZrO2 exhibits several well-defined sharp bands because of the symmetry reduction . In addition, the highly intense peaks at 292 and 636 cm−1 which are main characteristic bands of tetragonal ZrO2 cannot be found in the spectrum of the c-ZrO2 sample, which indicates the absence of tetragonal ZrO2 phase in this sample. Kontoyannis et al.  also reported that cubic ZrO2 shows amorphous-like Raman spectrum with one broad band at 530 to 670 cm−1. The features of Raman spectrum of c-ZrO2 as shown in Figure 2 is in accordance with the spectral results reported in the literature.
Transmission electron microscopy
High-resolution transmission electron microscopy
In order to authenticate the ZrO2 phase existed in the samples, high-resolution transmission electron microscopy (HRTEM) was carried out on particles of the three samples. Figure 3D represents the HRTEM image of the m-ZrO2 sample. The image clearly showed well-resolved lattice fringes. The distance between the fringes was calculated to be 0.297 nm which can be attributed to the interplanar spacing corresponding to (111) plane of monoclinic ZrO2 . The HRTEM image of t-ZrO2 was shown in Figure 3E. This image also showed well-resolved equidistant lattice fringes. The distance between the parallel fringes was calculated to be 0.296 nm which can be attributed to the well-recognized lattice d-spacing of (111) plane of tetragonal ZrO2 . A typical HRTEM image of particles of the c-ZrO2 sample is shown in Figure 3F. The image shows equidistant parallel fringes which depict single crystalline nature of the particle. The distance between the parallel fringes was calculated to be 0.291 nm which is the well-recognized lattice d-spacing of (111) plane of cubic ZrO2 .
BET surface area
The pore size distribution patterns of the synthesized ZrO2 samples were shown in the inset of Figure 4. Pore size distribution of the m-ZrO2 sample reveals a broad and monomodal distribution of the pore dimension in the mesoporous region. In addition, the c-ZrO2 sample showed a narrower pore size distribution than t-ZrO2. The porosity of the m-ZrO2 and t-ZrO2 samples appears to be arising from non-crystalline intra-aggregate voids and spaces formed as a result of inter-particle contact . The narrow and broad bimodal distribution of pores can be observed in the case of the c-ZrO2 sample. The porosity of this sample appears to be framework porosity which corresponds to the porosity within the uniform channels of ZrO2 structure.
Textural properties of the catalysts from N 2 adsorption measurements
S BET (m 2 g −1 )
V p (cm 3 g −1 )
Pore radius (Å)
X-ray photoelectron spectroscopy
Deconvolution of the spectra produces peaks attributed to the existence of two kinds of zirconium species, referred as Zr2+ species with low binding energy in the range 180.7 to 181.4 eV and Zr4+ species with higher binding energy in the range of 182.1 to 182.3 eV. It should be noted that the fraction of Zr4+ species for all samples is larger compared to that of species Zr2+. It is reported that the binding energy of Zr4+ species in pure ZrO2 is around 182.6 eV ; however, slightly lower values compared to that of stoichiometric ZrO2 were observed especially for the sample m-ZrO2 (182.1 eV), probably, due to some oxygen deficiency. The position shift toward the lower binding energy might be associated with the holes created by oxygen vacancies in the ZrO2 lattice .
Kawasaki  reported that Zr 3d components, Zr 3d 5/2 and Zr 3d 3/2 for cubic ZrO2 can be observed at 182.0 and 184.4 eV, respectively. The same components for tetragonal ZrO2 and monoclinic ZrO2 samples appeared at 182.7 and 184.7 eV  and 182.2 eV and 184.6 eV , respectively. The binding energy values of Zr 3d components observed in this study are in accordance with values reported in the literature.
Surface composition of catalysts from XPS measurements
Li et al.  indicated that the ZrO2 sample with pure monoclinic ZrO2 nanoparticles showed a pronounced absorption peak at 270 nm, and tetragonal and cubic ZrO2 nanoparticles show an absorption peak at 314 nm. The absorptions in the range 250 to 350 nm were assigned to O2 → Zr4+ charge transfer transitions with Zr in low coordination states (possibly six) either isolated or present in small ZrxOy clusters .
Band gap of all the ZrO2 samples was determined by establishing the relation between hυ and (αhυ)2. The obtained data indicated that the band gap energy for m-ZrO2 (3.25 eV) is lower compared with t-ZrO2 (3.58 eV) and c-ZrO2 (4.33 eV). Crystal structure plays an important role in the electronic structure of ZrO2. This effect is most significant in the d-electron-derived conduction bands (CBs). It is reported that the reduction of the CB gap between the Zr 4d (x2−y2, z2) and the Zr 4d (xy, yz, zx) CBs is present in cubic ZrO2 and disappears in tetragonal ZrO2, and also, substantial volume expansion was observed in the case of monoclinic ZrO2 due to the hybridization of Zr 4d CBs into a new single Zr 4d CB .
It was also reported that the pure tetragonal and monoclinic ZrO2 nanoparticles showed energy band gaps of 4.0 and 3.5 eV, respectively . These values are very similar to the values reported in the literature reports. Emeline et al.  determined an energy band gap of 5.0 eV for monoclinic ZrO2 thin films calcined at 550°C, and Chang and Doong  determined an energy gap of 5.7 eV for the same sample at the same temperature. However, Navio et al.  reported an energy band gap of 3.7 eV for monoclinic ZrO2 powders prepared by sol-gel method. These authors claim that the decrease in the band gap energy could be attributed to a highly disordered structure, as a result of the conditions used in the preparation technique. As a consequence of structural defects, some energy levels are introduced into the semiconductor band gap that allow transitions of lower energy and therefore lead to a decrease of the band gap energy.
Photocatalytic degradation of methyl orange
As mentioned in the experimental section, the catalyst was equilibrated with the methyl orange solution to check for adsorption of the dye on the solid photocatalyst. The spectra depicted in Figure 7 were recorded after the equilibration of the photocatalyst. The UV-vis absorption spectra of methyl orange have a strong characteristic peak at 465 nm and a weak absorption peak at 274 nm.
It was reported that the structures of nanoscale favor the movement or transfer of electrons and holes generated inside the crystals to the surface , which also enhances the photocatalytic activity. The photocatalytic activity of ZrO2 appears to be strongly dependent on the surface composition. Bachiller-Baeza et al.  reported that Lewis acid sites were more abundant on monoclinic ZrO2 than on tetragonal ZrO2, and the former brought about stronger surface adsorption sites concerning CO2 adsorption than the latter. Ma et al.  determined and compared the surface properties of ZrO2 polymorphs. It was found that ZrO2 polymorphs exhibited different surface hydroxyl and acid-base properties. These differences had great influence on the behavior of CO adsorption and reaction. They also showed that monoclinic ZrO2 possessed better adsorption properties than the other ZrO2 structures.
The adsorption capacity of methyl orange per gram of each catalyst was determined under identical conditions. It was observed that m-ZrO2 (1.95 mg g−1) possessed better adsorption capacity than the t-ZrO2 (1.05 mg g−1) and c-ZrO2 (0.65 mg g−1) samples. The photocatalytic activities observed in this study show similar trend that the m-ZrO2 sample showed high photocatalytic activity even though it possessed less surface area. ZrO2 nanomaterials have been investigated previously in the photocatalytic degradation of methyl orange; the time period required for the degradation of methyl orange tends to be 120 min or greater. Here, the synthesized pure monoclinic ZrO2 nanoparticles offered 99% of efficiency in 110 min of reaction time. The observed photocatalytic degradation activity is substantially higher than the activity reported for the ZrO2 samples in the literature.
It is known that usually high surface area of photocatalyst enhances dye adsorption and subsequent photocatalytic activity. However, it was also reported that the amount of dye adsorption on a catalyst also depends on the adsorption coefficient. Thus, a high adsorption coefficient on a low surface area material could lead to the same amount of adsorbed material per gram of catalyst as low adsorption coefficient on a high surface area material. This could be the reason why the rate (per gram basis) of methyl orange degradation is high for m-ZrO2 (low surface area) and c-ZrO2 (high surface area).
The m-ZrO2 sample possesses the smallest surface area (65 m2g−1) and largest pore size, while the c-ZrO2 has the largest surface area of 204 m2g−1 and smallest pore size. It is interesting that m-ZrO2 exhibited higher photcatalytic activity than c-ZrO2. Guo et al.  studied the influence of the pore structure of TiO2 on its photocatalytic performance. They observed that the photocatalytic activity of nanometer TiO2 is less than that of mesoporous TiO2.
Shao et al.  synthesized ZrO2-TiO2 composites which possessed different surface areas and textural properties. Composite samples showed surface area in the range of 270 to 80 m2g−1; however, the sample which has low surface area showed high photocatalytic activity due to it optimum Ti-Zr composition. It is clear from the literature reports that it is possible for catalyst, which possessed low surface area, to offer better photocatalytic activity than the catalyst which possessed high surface area. This is due to the fact that photocatalytic activity can be influenced by several other factors such as crytallinity, composition, particle size distribution, porosity, band gap, and surface hydroxyl density .
We also tested the reusability of the m-ZrO2 catalyst for subsequent cycles of methyl orange degradation under optimized reaction conditions. Many of the reported photocatalysts have not been used for further degradation studies due to the fact that they undergo photocorrosion, by the direct illumination with light, and hence their photostability is diminished for further runs. For the reusability study, we collected the white-colored catalyst remained after the reaction, washed, dried at 100°C for 30 min, and used it for further reactions. The catalyst was found to be active for 5 cycles without any major deactivation, and more than 95% degradation was achieved in all experiments within 110 min using the m-ZrO2 catalyst. The reusability of the m-ZrO2 nanoparticles was ascribed to the low photocorrosive effect and high catalytic stability of the synthesized m-ZrO2 sample.
Nanosize crystalline porous ZrO2 nanoparticles with pure monoclinic, tetragonal, and cubic phases were synthesized by different preparation methods. The photocatalytic performance of the three ZrO2 samples for the degradation of methyl orange was evaluated. Under the optimized reaction conditions, the m-ZrO2 sample comparatively showed a higher methyl orange degradation activity than the t-ZrO2 and c-ZrO2 samples. The pronounced photocatalytic activity for m-ZrO2 catalyst was mainly attributed to combining effects of factors including the presence of small amount of oxygen-deficient zirconium oxide phase, high crystallinity, broad pore size distribution, and high density of surface hydroxyl groups.
This project was funded by Saudi Basic Industries Corporation (SABIC) and the Deanship of Scientific Research (DSR), King Abdulaziz University, Jeddah, under grant number MS/14-325-1433. The authors therefore acknowledge with thanks SABIC and DSR technical and financial support.
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