Enhanced Red Emission in Ultrasound-Assisted Sol-Gel Derived ZnO/PMMA Nanocomposite.
Zinc oxide (ZnO) is a n-type semiconducting material with a great application potential as electron conduit in (opto) electronic devices [1, 2], photocatalysts [3, 4], and photoluminescence materials [5, 6]. There are several methods for the synthesis of ZnO nanostructures, including sol-gel method, controlled precipitation, solvothermal techniques, microemulsion, and sonochemical treatments . Among them, sonochemical synthesis has been emerged as an efficient technique to prepare ZnO NPs of different shapes [8, 9], ZnO polymer composites , and evenly doped ZnO NPs . In the sonochemical synthesis, the application of an ultrasound with a frequency ranging from 15 kHz to 10 MHz induces the formation, growth, and implosive collapse of bubbles in the reaction mixture, also known as cavitations . The collapse of bubbles induced by cavitations creates localized hotspots having extremely high temperature (5000 K), high pressure (500 atm), and rapid heating or cooling rate ([10.sup.9] K/s). These extreme conditions enable high-energy chemical processes such as formation of radical and high-surface-area nanocrystals and efficient diffusion of ionic dopants into crystals forming doped nanocrystals while keeping the apparent reaction conditions at room temperature and atmospheric pressure.
Many important applications of ZnO NPs rely on their optical properties. While ZnO absorb efficiently UV light with photon energy greater than its bandgap, of about 3.3 eV, it usually emits both UV and visible light. The UV emission is assigned to band-to-band recombination between electrons and holes residing at the edges of conduction and valence band, respectively. The visible emission is usually attributed to various recombination pathways between photoexcited charges being trapped at defect states within the bandgap. Although the chemical origin of defect states is still controversial [5, 13-15], surface modification has been widely used to control over the visible emission of ZnO, especially in ZnO nanostructures. Patrick Felbier and coworkers controlled air exposure of plasma-synthesized ZnO nanoparticles (NPs) to switch the emission from UV to yellow or green with a quantum yield of 60% . The changes in photoluminescence properties were reasoned to surface OH groups created during the exposure to air. Tang et al.  varied the density of oxygen vacancy and interstitial Zn on the surface of sol-gel derived ZnO NPs via adjusting pH of initial sol solution to change the emission color from green to orange. In addition to popularly observed green and orange emission, red emission ZnO NPs have been rarely reported [17, 18]. These representative examples point out a mean of control over the emission color of ZnO but also imply the high sensitivity of ZnO luminescence to environment.
Incorporation of ZnO into polymer matrix is a convenient way to stabilize the PL properties of ZnO and to add new functionalities to the polymer [6, 13, 19]. Herein, we observed unexpectedly that poly(methyl methacrylate) (PMMA) matrix quenches the original green-orange emission but enhances red emission of ZnO NPs. This result provides a simple ultrasound-assisted mixing method for fabrication of red-emitting composites for lighting applications.
2.1. Synthesis of ZnO Nanoparticles. An calculated amount of zinc acetate dihydrate (98%, Aldrich) was added into a flask containing a mixture of 95 ml ethanol (99.5%, Aldrich) and 5 ml DI water under [N.sub.2] environmental conditions. The mixture was then magnetically stirred to form a clear solution with a concentration ranging from 0.01 to 0.1 M. pH of the solution was adjusted to 9.5 by adding N[H.sub.3] solution (7 M, Aladdin Chemical). The reaction flask was connected with an ultrasonic Ti tip and placed into a thermostatic tank at 70[degrees]C. After being sonicated at a frequency of 20 kHz for two hours, the mixture was centrifuged at a speed of 8000 rpm to precipitate ZnO NPs, which were further rinsed with excess DI water and dried to perform powder ZnO.
2.2. Synthesis of ZnO-PMMA Composites. Powder ZnO and PMMA ([M.sub.n] = 54,000, Aldrich) were dispersed separately in dichloromethane by means of sonication to perform crude solutions. A calculated amount of ZnO crude solution was poured into PMMA solution and allowed to mix to form a homogenous composite solution with varied ZnO weight percentage. The solution was then poured on glass substrates, flatted by a glass tube, and dried to form composite membranes.
2.3. Characterizations. Crystalline structure of ZnO was studied by X-ray diffraction patterns recorded on a Bruker D5005 diffractometer. The morphology of ZnO NPs and ZnO-PMMA composites was investigated by scanning electron microscope (SEM) images which were obtained on a FEI NanoSEM 450. Transmittance electron microscope (TEM) images were obtained on JEOL TEM 4510 microscope. Optical properties of ZnO NPs and the resultant composites were characterized by UV-Vis absorption (Varian Cary 500 spectrometer) and photoluminescence (PL) measurements. For PL measurement, samples were excited with laser with a wavelength of 325 nm, and the PL signal was recorded by a Si-CCD detector-equipped monochromator (Horiba iHR550).
3. Results and Discussion
X-ray diffraction patterns of ZnO NPs obtained when varying the initial concentration of zinc acetate are shown in Figure 1. All samples exhibit common diffractions peaking at 2 theta of 31.7[degrees], 34.5[degrees], 36.3[degrees], 47.6[degrees], 56.7[degrees], and 63.9[degrees], which correspond to the reflection, respectively, from (100), (002), (101), (102), (110), and (103) lattice plans of ZnO wurtzite structure (JCPDS-36-1451).
The size of crystalline domains within ZnO NPs was estimated by using Scherrer's equation: D = k[lambda]/([beta] cos ([theta])), where [lambda] = 0.1542 nm is the wavelength of incident X-ray, [beta] is the full width at half maximum of the (101) peak, [theta] is the Bragg diffraction angel, and k = 0.9 is the constant . It was 45 nm, 35 nm, and 29 nm for ZnO NPs synthesized from 0.1 M, 0.05 M, and 0.02 M zinc acetate solutions, respectively. These domain sizes were much smaller than the dimension of ZnO NPs observed in SEM images shown in Figure 2. Most of ZnO NPs synthesized from zinc acetate 0.1 M solution have a rod-like hexagonal structure with 1 [mu] (width) x 2.5 [mu] (length) dimension (Figure 2(a)). When the concentration of precursor solution decreased, the ZnO NPs turned into spherical with a diameter of 300 [+ or -] 50 nm as shown in Figures 2(b) and 2(c). The results suggest a simple tool, that is, varying the concentration of precursor solution, to control over the morphology and size of sol-gel derived ZnO NPs. In line with X-ray analysis that ZnO NPs had crystalline domains of 29 / 45 nm, the TEM image of a ZnO particle shown in Figure 2(d) reveals many connecting ZnO domains within one particle.
The extreme reaction conditions, for example, high temperatures, pressure, and heating and cooling rates, induced by collapse of microbubbles in ultrasound irradiated solution have been utilized to prepare various ZnO nanostructures [8, 21, 22]. Ultrasonication conditions (intensity, duration, temperature, and duty cycle) and chemical composition (solvent and additives) are proposed to be the key parameters of controlling over the morphology of ZnO nanostructures. In the present study, we observed that ZnO changed from spherical particle to hexagonal rod-like structure when only the concentration of zinc acetate increased from 0.02 to 0.1 M (Figure 2). The formation of ZnO nanostructures can be represented as follows:
N[H.sub.3] + [H.sub.2]O [right arrow] N[H.sup.+.sub.4] + O[H.sup.-] (l)
Zn[(OOC[H.sub.3]).sub.2] + 2O[H.sup.-] [right arrow] Zn[(OH).sub.2] + 2C[H.sub.3]C[O.sup.O-] (2)
Zn[(OH).sub.2] + 4N[H.sub.3] [??] [Zn[(N[H.sub.3]).sup.2+.sub.4]] + 2O[H.sup.-] (3)
Zn[(OH).sub.2] [right arrow] ZnO + [H.sub.2]O (4)
At pH of 9.5 and temperature of 70[degrees]C (see Experimental), Zn[(OH).sub.2] are the major soluble species of [Zn.sup.2+] complexes (2) . The presence of N[H.sub.3] (3) and ultrasound irradiation inhibited fast aggregation of neutrally charged Zn [(OH).sub.2] into amorphous solids. Furthermore, ultrasonication induced the condensation of Zn[(OH).sub.2] into ZnO nanocrystals according to (4). This process took part homogeneously in all the volume of reaction forming spherical ZnO NPs when the concentration of the zinc precursor was low, for example, 0.02 or 0.05 M. It was reported that the presence of Zn[(OH).sub.2] is a key factor for the growth of ZnO nanocrystals into hexagonal nanorods by adding Zn[(OH).sub.x] complexes onto positively charged, Zn-terminated (0001) planes [22-24]. Similarly, when the concentration of the zinc precursor increased to 0.1 M, free Zn[(OH).sub.2] reacted with preformed spherical ZnO nanocrystals producing hexagonal rod-like structures as seen in Figure 2(a). The presence of Zn-OH terminals on the surface of ZnO NPs needed for the growth of ZnO rod-like structures is supported by the FT-IR spectrum of ZnO shown in Figure 3(a). A broad absorption band centered at 3400 [cm.sup.-1] and a shoulder at 1560 [cm.sup.-1] can be attributed to vibrations of O-H bonds in either absorbed water or surface Zn-OH groups, which is further supported by a shoulder at 1630 [cm.sup.-1]. A peak at 1385 [cm.sup.-1] is resulted from O[H.sup.-] absorption of hydrogen-related defects .
Optical properties of ZnO NPs are summarized in Figures 3(b) and 3(c). ZnO NPs absorbs efficiently UV light with wavelength less than 400 nm, demonstrating the UV-blocking property. Direct bandgap of ZnO, [E.sub.g] = 3.18 eV, was determined by Tauc expression (inset in Figure 2(b)): [([alpha]hv)).sup.2] = B(hv - [E.sub.g]), where [alpha], hv, and B are the absorption coefficient, photon energy, and constant, respectively . PL spectra of ZnO NPs shown in Figure 3(c) exhibit two distinct UV and visible emission regions. The UV emission is relatively narrow, maximizes at 385 nm, and decreases in intensity when drying the ZnO NPs in the open-air conditions. The visible emission is broad, ranging from 450 nm to 800 nm. Additionally, drying ZnO NPs in air at middle temperatures, for example, 100 [degrees]C, quenches completely the UV emission while enhances the visible emission. The results promise the use of sol-gel derived ZnO NPs as white-light phosphor in LED applications.
Morphology and optical properties of the solvent-mixed ZnO-PMMA composite are summarized in Figure 4. Composite membrane fabricated by a bar-coating method was relatively homogeneous with some white spots (Figure 4(a)). The SEM image shown in Figure 4(b) visualized at a white spot revealed aggregates of ZnO NPs with physical cracks. This phase segregation may be due to large aggregations of ZnO NPs that were still present in the solvent-mixing phase and difference in hydrophilicity between ZnO NPs and PMMA [19, 27, 28]. Due to this phase segregation, we restricted our study to ZnO-PMMA composites with ZnO composition of less than 1 wt.%.
UV-Vis absorption property of a 90 p thick ZnO-PMMA membrane is shown in Figure 4(c). In addition to sharp UV absorbance that increased with ZnO content, the transmittance spectra exhibit a tail increasing gradually with wavelength. The absorbance in the UV region of the composite received from UV-blocking property of ZnO. The absorption tail can be attributed to light-scattering effect derived from phase separation in the ZnO-PMMA composite discussed earlier.
PL spectra of the ZnO-PMMA composite are shown in Figure 4(d) in comparison with PMMA alone. Both PMMA and ZnO-PMMA composites exhibit an intense and unsymmetrical peak at 390 nm probably due to unknown impurities. Unfortunately, this blue emission may overwhelm possible band-edge emission from ZnO NPs as seen in Figure 3(d). The 1 wt.% ZnO-PMMA sample showed a combined PL feature between the UV-blue emission from PMMA matrix and the broad visible emission from ZnO powder (Figure 3(d)). Interestingly, when the content of ZnO NPs decreased to 0.6 wt.%, only red emission centered at 702 nm was observed in the visible region. Further decreasing the content of ZnO NP to 0.2 wt.%, the intensity of red emission was too low as compared with the UV-blue emission from PMMA matrix.
Visible emission is widely observed on ZnO nanostructures and has been assigned to the recombinations of photoexcited electrons--holes being trapped at defect states including oxygen vacancies ([V.sub.O]), zinc interstitials ([I.sub.Zn]), zinc vacancies ([V.sub.Zn]), and their complexes [2, 6, 14, 16, 17, 20, 29-31]. Here, we put forward a plausible mechanism shown in Figure 5 to explain PL properties of the ZnO-PMMA composite.
The presence of [I.sub.Zn] defect states whose energy level is theoretical predicted to be near the conduction band minimum results in charged [I.sup.+.sub.Zn] and [I.sup.+.sub.Zn] . Both [I.sub.Zn] and [V.sub.O] related point defects have a high formation energy leading to their low concentrations in ZnO. However, Coulomb interaction between [I.sub.Zn] and [V.sub.O] point defects efficiently reduces their formation enthalpy and results in a series of hybridized [I.sup.*.sub.Zn] and [V.sup.*.sub.O] states whose energies vary as a function of their mutual separation . The existence of [I.sup.*.sub.Zn] related states was experimentally observed by UV-blue emission in ZnO NPs when excitation energies just below the energy gap were applied . In the present study, we did not observe such UV-blue emission on ZnO NPs (Figure 3(c)), probably due to a high-energy excitation at 325 nm (3.81 eV). [I.sub.Zn]/[I.sup.*.sub.Zn] and [V.sup.++.sub.O] related sates are localized about 0.1-0.6 eV and 2.0 eV, respectively, below the conduction band minimum, and that [V.sup.+.sub.O] states are aligned at about 2.4 eV above the valence band maximum [30-32]. These defect states are depicted in Figure 5(a), and the energies are noted in Figures 3(c) and 4(d). In Figure 5(a), we tentatively assigned the green (2.4 eV) emission to the recombination between photoexcited electrons being trapped at [V.sup.+.sub.O] states and valence holes. The orange (2.0 eV) and red (1.77 eV) emission is attributed to recombination between holes being trapped at [V.sup.++.sub.O] states and electron residing at [I.sub.Zn] related states and conduction band edge, respectively. The ionized oxygen vacancies effectively manifest at ZnO NPs grain boundaries as discussed previously from the TEM image of ZnO NPs in Figure 2(d). The hybridization between [I.sub.Zn] and charged [V.sub.O] states varied their energy levels within the bandgap giving rise to a broad emission from 450 to 800 nm as seen in Figure 3(c). This emission feature was still observed in the ZnO-PMMA composite with 1 wt.% of ZnO where the grain boundary among the ZnO phase is still significant (Figure 4(d)). In addition to the grain boundary, Zn-OH groups on the surfaces of ZnO NPs (Figure 3(a)) also contribute to the broad orange emission of ZnO NPs .
Now, we are going to explain the enhanced red emission observed in ZnO-PMMA with 0.6 wt.% of ZnO (Figure 4(d)) by using a band-bending model that is schematically illustrated in Figure 5(c). Theoretical calculation on the local structure of oxygen vacancies shows that, in neutral state ([V.sub.O]), four surrounding Zn atoms relax inward by 12% of the equilibrium Zn-O bond while in [V.sup.+.sub.O] and [V.sup.++.sub.O] states these atoms relax outward by 3% and 23%, respectively . The relaxation direction is depicted in Figure 5(b). In the present study, the ZnO-PMMA composite was prepared under ultrasonication conditions, which can efficiently induce the formation of -COOH groups within PMMA matrix and the reaction: Zn - OH [+ or -] COOH [right arrow] Zn - OOC + [H.sub.2]O . The Zn-OOC bonds between ZnO NPs and PMMA matrix stabilized chemically the [V.sup.++.sub.O] states. The absence of the vibrational bands of surface Zn-OH groups at 3400 [cm.sup.-1] and 1385 [cm.sup.-1] in FT-IR spectra of the ZnO-PMMA composite (Figure 3(a)) supports this reaction. Additionally, the negatively charged -CO[O.sup.-] groups bend the band of ZnO upward, resulting in a depletion of the interface region where formation energy of [V.sup.++.sub.O] is efficiently reduced [32, 33, 35]. We suppose that the band bending increased the concentration of [V.sup.++.sub.O] states to an extent that captured most of photoexcited holes, and at the same time they, in turn, increased the concentration of [I.sub.Zn] related states via Coulomb interaction. As a result, recombination between electrons and holes being trapped at [I.sub.Zn] and [V.sup.++.sub.O] states, respectively, became the major emission channel in the ZnO-PMMA composite as seen in Figure 4(d).
By using ultrasonic irradiation, we were able to prepare ZnO particles with different shape, from spherical particles to hexagonal rod-like structures, by simply changing the concentration of the zinc acetate precursor. The resultant ZnO NPs showed a broad orange emission originated from [I.sub.Zn] and [V.sub.O] trapping defects together with a low-intensity, band-edge peak in the UV region. Increases in [I.sub.Zn] and [V.sup.++.sub.O] concentrations induced by band-bending effects as embedding ZnO NPs into PMMA matrix accounted for the enhanced red emission in the ZnO-PMMA composite. The results demonstrated in this study can be utilized for the development of ZnO nanostructures as well as their composite for diverse lighting applications.
Conflicts of Interest
The authors declare that they have no conflicts of interest.
This research was supported by Hanoi Pedagogical University No. 2 under Grant number C.2017-18-05.
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Van-Tuan Mai, (1) Quang-Bac Hoang (iD), (2) and Xuan-Dung Mai (iD) (2,3)
(1) Department of Basic Sciences, Electric Power University, 235 Hoang Quoc Viet, Hanoi, Vietnam
(2) Department of Chemistry, Hanoi Pedagogical University No. 2, Xuan Hoa, Phuc Yen, Vinh Phuc, Vietnam
(3) Institute of Research and Development, Duy Tan University, 03 Quang Trung, Da Nang, Vietnam
Correspondence should be addressed to Xuan-Dung Mai; email@example.com
Received 6 July 2017; Revised 27 October 2017; Accepted 28 November 2017; Published 7 February 2018
Academic Editor: Marco Cannas
Caption: Figure 1: X-ray diffraction patterns of ZnO nanoparticles when varying zinc acetate concentration.
Caption: Figure 2: SEM images of ZnO nanoparticles obtained by using (a) 0.1 M, (b) 0.05 M, and (c) 0.02 M zinc acetate. (d) TEM image of ZnO NPs.
Caption: Figure 3: (a) FT-IR spectra and (b) UV-absorption. Inset: Tauc plot determining the bandgap of ZnO. (c) PL spectra of ZnO samples with different postdrying conditions ([[lambda].sub.ex] = 325 nm).
Caption: Figure 4: (a) A membrane picture; (b) SEM image; (c) UV-Vis absorption; (d) photoluminescence spectra of the ZnO-PMMA composite.
Caption: Figure 5: (a) PL mechanism in the ZnO-PMMA composite; (b) stabilization of [V.sup.++.sub.O] induced by PMMA matrix; (c) band bending at ZnO-PMMA interfaces.
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|Title Annotation:||Research Article|
|Author:||Mai, Van-Tuan; Hoang, Quang-Bac; Mai, Xuan-Dung|
|Publication:||Advances in Materials Science and Engineering|
|Date:||Jan 1, 2018|
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