Photocatalytic Activity and Nano Structural Investigation on Co3O4 Nanoparticles

Document Type: Research Paper

Author

Department of Engineering, Tonekabon Branch, Islamic Azad University, Tonekabon, Iran

Abstract

In this study, Co3O4 nanostructure is synthesized from the Co(NO3)2.6H2O reactant through  co-precipitation technique, and then is calcined at different calcination temperatures (CTs).The XRD peak broadening and its corresponding properties, such as lattice stress, dislocation density, X-ray density, specific area of cubic Co3O4 nanocrystallites, and deformation energy density are analyzed using uniform deformation model (UDM), uniform deformation stress model (UDSM), uniform deformation energy density model (UDEDM), and size-strain plot (SSP) method. Based on the XRD results, the strain of the nanocrystallites increases with the increase of CT. The lattice, structural properties, and morphology of the nanoparticles (NPs) during the CT are studied. NPs calcined at 700 oC show the most lattice strain, stress, and deformation energy, and the least X-ray density and specific area. The photocatalytic activity of Co3O4 (NPs) is specified by the decoloration of methylene blue (MB). Based on the results, the Co3O4 NPs calcined at 700 oC show the most photocatalytic activity. Furthermore, the activation energy of NPs, surface topography, pore size distribution, specific surface area, and crystallization of phases, during thermal treatment, are investigated by the BJH and BET methods. 

Keywords


INTRODUCTION

Recently, Co3O4 nanoparticles have been widely used in various applications of medical, industry, data storage devices, catalysts, photocatalyst, gas sensors, rechargeable batteries, pigments, magnetic fluids, and optical thin films [1-3]. Co3Ois a transition metal oxide and p-type semiconductor that has been attractively considered for its optical, electrical, and magnetic properties due to different states of cobalt in oxygen absorbed [4]. The physical, chemical properties and performances of Co3O4 nanoparticles (NPs) in mentioned applications intensively depend on the particle size, shape, geometry, dimension, and morphology [5]. Various routes and methods have been made for fabricating Co3O4 NPs, including pulsed laser deposition [6], chemical spray pyrolysis [7, 8], sol-gel method [9], solvo-thermal [10], reduction-oxidation route [11], cobalt salt decomposition [12], hydrothermal [13], chemical combustion [14] and mechanochemical method [15]. Most of the above-mentioned methods are complex, expensive and inconvenient to synthesize of Co3O4 NPs. Even though the sol-gel method seems to be a low cost processes, it has some disadvantages and limitations due to high-temperature synthesis conditions and less homogeneity. Among all the above methods, co-precipitation is accompanied by low cost, low temperature, high yields of product, versatile, and needs to fewer solvents, decrease pollutions, high controlling, and great chemical homogeneity [16,17].

Conventional oxidation methods are unable to eliminate the complex organic pollutants especially textile dyes. The advanced oxidation processes (AOPs) have been drastically degraded the harmful and indecomposable chemical compounds to smaller and nature-friendly compounds via highly reactive radicals  [18-20]. The Co3O4 NPs have an acceptable photocatalytic activity of dyes such as methylene blue.

This research focuses on the synthesis of Co3O4 NPs by co-precipitation method without using any templates, catalysts and contaminations; furthermore, it investigates the effect of CT on the strain, morphology and photocatalytic activity of Co3O4 NPs. The degradation rate of methylene blue in an aqueous solution contains Co3O4 NPs under UV. exposure which is assigned as a measure of its photocatalytic activity.

EXPERIMENTAL PROCEDURES AND DETAILS

The precursor materials and experimental conditions used for Co3Onanoparticles synthesized by the co-precipitation method are Co(NO3)2.6H2O (Merck , ethanol (Merck , deionized water, and HNO(Merck . The molar ratio of precursors is Co(NO3)2.6H2O /HNO3/H2O=1:4:2. First, cobalt nitrate is dissolved in deionized water and vigorously stirred with a magnetic stirrer. Afterward, HNO3 is dropped accurately to the starting solution and adjusted at pH=4. The solution is ultrasonicated for 10 min at 45 kHz (model: Sono Swiss). A purple solution emerges, and it is stirred for about 60 h until a dark precipitate appears. Subsequently, the precipitation is dried in the oven for 12 h at 85 oC and rinsed several times thoroughly with deionized water to eliminate any pollutants and residual ions. The rinsed precipitation is dried again. The dark purple cobalt hydroxide solid is grounded in an agate mortar for 10 min to form a fine powder. Afterward, the powder is calcined at 400, 500, 600 and 700 oC with 15 Co/min heat gradient, stayed for 2 h and cooled down with the same condition.

The X-ray diffraction (XRD) is applied (GBC-MMA) using Kα(Cu) radiation λ= 0.1540 nm, 0.02o step size and 10 deg/min exposure speed. XRD patterns are recorded from 10-80o. The particle size and structure of the nanocrystallites are determined from transmission electron microscopy (TEM, model: Philips, CM120). Scanning electron microscopy (SEM, model: Hitachi S-4160) equipped by EDX is utilized to take images of nanoparticles. The FTIR spectrum is recorded on (model: Perkin-Elmer 783) with the sample as KBr thin tablet. The photodegradation of MB is carried out under UV. exposure (model: Philips, 254 nm, 33.6 mw/cm2). The photocatalytic activity of Co3O4 nanopowders is determined by decoloration of MB and measured with UV.-Vis. spectrophotometer (model: Varian 50 scan). All experimental procedures and concentration of Co3O4 as a photocatalyst and MB are cited in our previous work [21,22]. The temperature of the photoreactor is fixed at 27.0 ± 0.5 oC by a small ventilator. The reaction stock solution is provided by adding 30 mg of Co3O4 nanopowders calcined at different CTs into 100 ml MB aqueous solution.

RESULTS AND DISCUSSION

The XRD patterns of the precipitate calcined at 400, 500, 600 and 700 oC are revealed in Fig. 1. As seen, all prominent peaks intensities of (111), (220), (311), (222), (511) and (440) could confirm to a Co3Ocubic crystallite phase (Space group: Fd3m and lattice parameter, a= 8.08 ). These peaks and corresponding angles (2θ) show acceptable agreement with the Joint Committee on Powder Diffraction Standards data [JCPDS-42-1467] [23]. The interplanar space values and Miller indices can be obtained from the Bragg formula (nλ=2d sin θ). The cubic lattice constant (a) and cubic cell volume of Co3O4 nanoparticles (V), calculated from the lattice geometry equation, Equation 1, are tabulated in Table 1, as follow:

 (1)

 (2)

 (3)

 (4)

where M is the molecular weight, a is the cubic lattice constant, N denotes Avogadro’s constant and L is the Co3O4 nanocrystallite size. As seen in Table 1, the estimated values of Dincrease by increasing the CT while, the values of Sdecrease by increasing the crystallite size and CT.

The dislocation density () is defined as the number of defects in the crystallite lattice that could be estimated by the experimental relationship with the crystallite size from Equation (5):

 (5)

where L is the crystallite size. As shown in Table 1, the dislocation density of the Co3O4 nanocrystallites decreases by increasing the CT and nanocrystallite size.

It is worth noting that peak width broadening due to instrumental amplification causes to increase the size and lattice strain of nanocrystallites [24]. In order to eliminate the instrumental contribution
() of measured broadening (), the line broadening of standard material such as silicon is utilized. The corrected instrumental broadening associated with the diffraction peak of cubic Co3O4 nanoparticles is estimated by using the following equation:

 (6)

There are not any extra peaks that correspond to impurities and uninvited materials. The intensity of diffraction peaks increases with increasing CT. This increase is attributed to the improvement of crystallinity quality, thermal stability and growth of boundaries. According to Fig. 1, low CT shows less peak intensity as well as a low degree of crystallization. The Co3O4 crystallite grain size is measured from the broadening of the peaks correspond to the Scherrer equation:

 (7)

therein, L is the crystallite size (nm), β is the full width at half maximum of peaks (radians), λ is the wavelength of CuKα (1.54 ) and θ is the Bragg’s angle corresponding to prominent and maximum intensity peak (311) at 2θ= 37.1o. As shown in Table 1, the average crystallite size increases by increasing the CT. This enlargement is due to the growth of the grain boundaries and increasing the rate of crystallite nucleation. This implies that the size distribution could be controlled by varying the CT. Table 1 presents the XRD data of the Co3O4 crystallite phase. The Sherrer equation considers only the instrumental corrected broadening corresponding to crystallite size without strain effect.

Williamson-Hall (W-H) method attributes the peak broadening not only to the contribution of nanocrystallite size but probably also to the strain and lattice defects. This assumption could be represented as:

 (8)

 (9)

 (10)

where  denotes the total breadth of diffraction peak,  is the corrected instrumental broadening,  is the micro-strain contribution of broadening, is the elastic lattice strain, shape factor k is 0.94 to Scherrer’s shape factor and λ= 0.1540 nm. According to the above assumption, uniform deformation method (UDM) consider the strain to be uniform in all crystallographic directions. The UDM plot is depicted with ( in terms of the associated values of ( for the preferred orientation peaks for different CTs (Fig. 2(a)). The values of nanocrystallite size and elastic lattice strain are calculated from the Y-intercept and slope of the fitted line.

According to uniform stress deformation Method (USDM), based on the generalized Hook’s law and anisotropic nature of crystallite structure, there is a linear relationship between elastic lattice strain (ε) and lattice stress (σ) that is expressed by:

 (11)

 (12)

where  is the Young’s modulus in the direction perpendicular to the lattice plane (hkl) associated with the mentioned prominent peaks. The validity of this method is in the range of low strain.

The Young’s modulus and relationship with its elastic compliances (Sij) are given by the following formula:

,

 

 (13)

where S11 , S12 and S44 are the elastic compliances of the Co3O4 cubic crystallite phase and their values are estimated as 4.99, -2.36 and 14.08 (Tpa)-1, respectively [25]. The Young’s modulus (Ehkl is determined to be about 209.07 GPa for (111), 206.82 GPa for (220), 204.41 GPa for (311), 209.07 GPa for (222), 200.40 GPa for (400), 206.91 GPa for (422), 202.18 GPa for (511) and 206.82 GPa for (440). The average Young’s modulus () value for the Co3O4 cubic crystallite phase is calculated as 205.71 GPa.

As seen in Fig. 2(b), the uniform deformation stress () and crystallite size could be calculated from the slope and Y-intercept of the fitted line depicted between  and , respectively.

Accepting the homogeneity and isotropy nature of crystallites is not correct in many cases. Furthermore, the linear dependency between stress and strain through the Young’s modulus and generalized Hook low () could be considered to determine the deformation energy density (u). Therefore, the modified form of Eq. (12) is given by:

 (14)

Fig. 2(c) indicates the plot of  versus . According to the plot, u and L could be calculated from the slope and Y-intercept of the fitted line, respectively. The W-H models consider the isotropic peak broadening due to isotropic diffraction domains and micro-strain contributions. In the condition of isotropic line broadening, it is possible to acquire a beneficial assessment of size-strain parameters by regarding an average size-strain plot (SSP). According to this approach, more contribution and influence are assigned to the low-angle reflections, where the accuracy and precision are generally more than the high-angle data. This selective election reduces the scattering of data points around the linear fitted line in size-strain plot. Halder-Wanger model assumes that the profiles of the size and lattice strain are characterized by a Lorentzian and Gaussian function, respectively [26]. Accordingly, the SSP method can be written as:

 (15)

where k is a shape constant for spherical and regarded as 4/3. As indicated in Fig. 3,  versus  for the all intensive peaks of Co3O4 cubic crystallite phase is plotted. The mean value of the strain and crystallite size is determined by the y-intercept and slope of linear fitted data, respectively. The resulted data from the W-H and H-W methods are summarized in Table 2.

There is a proper linear relationship due to the existence of good crystallization at high CTs. As seen in Figs. 2 and 3, the elastic lattice strain increases with increasing the CT in all elastic deformation models. This increase is attributed to the more broadening and more grain boundaries. By increasing the CTs, it is possible to produce the required energy by the atoms to locate an appropriate position in constructing the crystallite phases [26]. The lattice strain changes d-values of diffracting planes. Nanocrystallites reveal more broadening in comparison with bulk materials due to lesser lattice planes, participating in the broadening of peaks. The broadness of peaks could occur because of lattice defects, crystal imperfection, dislocations, stacking faults, terrace vacancy and terraces. The growth process drastically affects on lattice strain. In this process, chemical bonds and ligands possess insufficient time and activation energy to diffuse to appropriate positions and sites [27-29].

The morphology of the samples that are synthesized by precipitation method is revealed with different CTs. Fig. 4(a-d) reveals morphology and remarkable aggregation of particles at low CTs. As seen, nanoparticles show less agglomeration and density with increasing CT, so that form bigger particles in the porous materials. As the CT gradually is raised from 400 oC to 700 oC, the average size of nanoparticles increases, which agrees with the XRD results. The SEM images show that the particles are somewhat spherical in shape at low CTs. The EDX pattern reveals the present chemical composition as well as the purity of Co3O4 nanoparticles (Fig. 5).

The total energy of Co3O4 nanoparticle formation could be derived by using the Scott [30] equation:

 (16)

where L is the average nanocrystallite size, E is the activation energy, R is the ideal gas constant, C is the constant of relation and T is the absolute temperature correspond to CTs.

The variation of Ln(L) versus 1/T is plotted and fitted as a straight line (Fig. 6). It is supposed that Scott equation applied in the homogenous and unified growth of grains which explains the growth rate of crystalline grain from amorphous shape during thermal treatment. The activation energy of Co3O4 nanocrystallites during calcination is calculated to be 14.79 KJ/mol.

In order to study the chemical bonds in Co3Onanoparticles, the FT-IR spectra are carried out in the range of IR (400-4000 cm-1). As shown in Fig. 7, the spectrum of the calcined Co3Onanoparticles reveals a broad absorption band in the range of 1650 and 3400-3600 cm-1, which is attributed to the asymmetrical and symmetrical OH bonds from co-ordinated or entrapped water. The intensity of this band decreases and evades as the CTs increases. As seen in Fig. 7, the vibration of Co+3 ions in octahedral holes appears at 570 cm-1, and the stretching vibration in the Co+2 ions in the tetrahedral holes reveals at 655 cm-1. These bands predicate the presence of FCC (face-centered cubic) nanocrystalline structure of Co3Onanoparticles [1,5,31].

Fig. 8 shows the TEM images of structure and morphology of Co3O4 nanoparticles calcined at different CTs. This figure reveals that by increasing the CTs, the growth and aggregation of nanoparticles will be augmented. The average size of nanoparticles are 40, 57, 70 and 82 nm for samples calcined at 400, 500, 600 and 700 oC, respectively. This growth is in an acceptable agreement with the XRD and SEM analyses. The samples calcined at low temperatures are partially congested, agglomerated and reveal spherical shape. By increasing the CTs, the boundaries and surface of adjacent particles interpenetrate, causing to enlarge the diameter and the size of nanoparticles, while they are partially granular, uniform and cubic [32,33].

The photocatalytic activity of the photocatalyst solution is determined by the UV.-Vis. spectro-photometer at 666 nm as revealed in the inset graph of Fig. 9. Fig. 9 indicates the time-dependent absorption spectra of MB located at . The intensity of absorption plots gradually decreases with increasing the irradiation time because of the dye decoloration. This plot shows the dependence of C/C0 versus the time irradiation 0 to 50 minutes and illustrates the photodegradation percentage after 50 min that are about 80%, 89%, 93%, 96% for samples were calcined at 400 oC, 500 oC, 600 oC and 700 oC, respectively.

The degradation rate of the aqueous solution of MB by Co3O4 NPs under UV irradiation is calculated by the equations mentioned below:

 (17)

 (18)

The comparative concentration of MB in the logarithmic scale  is plotted against UV.-Vis. exposure time according to samples calcined at different CTs (Fig. 11). The slope of logarithmic plots is the rate constant of photodegradation [34]. The Photocatalytic measurements in Table 3 reveal the relevant kinetic variables, such as correlation coefficient (R2) and the degradation rate constant (k). All reactions reveal a linear relation. As seen in Fig. 11, the rate constant, k is estimated depending on the presence of Co3O4 and CTs. By increasing the CTs and increasing the porosity of samples, the rate constant (k) increases, since more crystallinity of Co3Ocrystalline phase has an outstanding effect on the degradation of the organic complex compounds. Furthermore, the enhancement in photocatalytic efficiency has been imputed to improved thermal stability, the surface properties, surface porosity and ultimate results to generate the instant splitting of photo-induced electrons and holes and prolonging the recombination process of conduction and valence band carriers.

Fig. 11 shows the N2 physisorption isotherm, Brunaur-Emmett-Teller (BET) and Barret-Joyner-Halenda (BJH) pore size distribution for the Co3O4 nanoparticles that were calcined at 700 oC. According to the adsorption-desorption (ads-des) isotherm, the Co3O4 nanoparticles show the IV type characteristic portends that they are microporous join with mesoporous structure. The BET specific surface area (SBET), total pore volume, mean pore diameter, and pore diameter at peak of the BJH curve (rp,peak) are derived and shown in Table 4. rp,peak shows the peak of the size in pore size distribution. The ads-des curves show the hysteresis loop that indicates the formation of cylindrical pores and capillary condensation in meso and micropores. The first knee indicates the approximate position of monolayer and the second knee indicates the formation of the multilayer.

CONCLUSION

The Co3O4 NPs were synthesized by the co-precipitation method. The nanostructure and photocatalytic performance of the prepared Co3O4 NPs such as the size, strain and photocatalytic activity were investigated. The CTs affected the nanostructural and optical properties. The XRD, SEM and TEM analysis revealed that average sizes of nanocrystallites increase by raising the CTs. The EDX pattern showed the presence of chemical elements as well as the purity of the Co3Onanoparticles. The XRD analysis indicated a low degree of crystallinity for samples calcined at low temperatures. The line broadening of the Co3O4 cubic crystallite phase related to the crystallite size and lattice strain were investigated by the W-H and H-W methods with a different assumption about the isotropic and homogeneity nature of the crystallite. Accordingly, the crystallite size, lattice strain, stress, and uniform deformation energy of the Co3O4 cubic crystallite phase were determined. Based on the results, the crystallite size, lattice strain, stress, and deformation energy increased as CT increased. By increasing the CT, the X-ray density and specific area of Co3O4 cubic crystallite phase decreased. The SEM images of the NPs showed sphere-like particles and more congestion compared to the samples calcined at higher temperatures. The activation energy of Co3O4 was estimated to be 14.79 KJ/mol. The experimental results showed that decomposition of methylene blue under UV. irradiation had a higher photocatalytic activity by increasing the CT. The ads-des curves predicted the formation of cylindrical pores and capillary condensation in meso and micropores. The first and second knees of the ads-des plot indicated the approximate position of monolayer and the formation of multilayer, respectively. Therefore, Co3O4 nanoparticles could be a promising candidate to act as a gas absorbent in gas sensors. Based on the results presented, Co3O4 N Ps show a higher photocatalytic activity, less lattice strain and more thermal durability with increasing the CTs.

ACKNOWLEDGMENT

The author appreciates Islamic Azad University, Tonekabon Branch for its financial support throughout this research project.

CONFLICT OF INTEREST

The authors confirm that this article content has no conflict of interest.

 

 
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