The Optical and Microstructural Characterization of the Polymeric Thin Films with Self-Assembly Nanoparticles Prepared by Spin-Coating Techniques

: anhydride-poly(ethylene glycol) co-polymer (A-PEGCP) has been synthesized from maleic anhydride, poly(ethylene glycol) and bisphenol-A diglycidyl ether without using any organic solvent. The thin ﬁlms produced from A-PEGCP solution were spin-coated on ITO-coated glass. The nanoparticles are observed in the thin ﬁlms. It is proposed that the nanoparticle is built by a self-assembly process with bisphenol-A aggregates and poly (ethylene glycol) moieties. The e ﬀ ects of concentration, thermal annealing, excitation wavelength and moisture on the optical and nanostructured characterization of the thin ﬁlms are investigated in this study. Photoluminescence (PL) spectrum of the thin ﬁlm on ITO-coated glass has a peak of about 450 nm that extends from 360 to 550 nm under 325 nm excitation. The increase in PL intensity is accompanied by a red shift of PL spectrum as concentration increases. Moreover, the slightly red shift of PL spectrum is also observed as annealing temperature increases. Meanwhile, PL intensity negligibly decreases with annealing temperature. The degradation in PL intensity is apparent due to moisture. The excitation-wavelength dependent photoluminescence (EWDP) is observed in the thin ﬁlm. UV-Vis absorption spectra of the thin ﬁlms are red-shifted with concentration due to more molecular aggregation. The highest occupied molecular orbital (HOMO) energy is − 9.52 eV. The optical band-gap energy is 4.09–4.44 eV.


Introduction
In the past decade intensive attention has been paid to organic materials for their potential applications in flexible displays and solid-state lighting [1][2][3][4][5][6][7][8]. Specifically, for organic compounds with large molecular mass, wet-processing techniques are more suitable and developed in industry. Polymer light-emitting diodes (PLEDs) exhibit lower power consumption, faster response times, larger viewing angles, smaller sizes and greater ranges of color and contrast, along with being inexpensive and rapid to produce. Therefore, it provides simple manufacturing processes such as spin coating [9][10][11][12] or ink-jet printing [13][14][15][16][17][18][19] to produce large area displays or lighting. Nevertheless, PLEDs still suffer from lower performances in terms of their reliability and lifetime. Moreover, large molecular organic compounds are mainly π-conjugated materials. Generally, π-conjugated polymers are prepared by polycondensation based on catalytic cross-coupling reactions. However, the pre-preparation of organometallic reagents and by-production of a stoichiometric amount of toxic compounds are often involved in the cross-coupling reactions. These disadvantages have been a concern in industrial applications. Thus, new polymers are increasingly designed and synthesized [20][21][22][23][24][25][26][27][28][29][30][31][32]. In addition,

Results and Discussion
In general, organic solvents are volatile, flammable and toxic. However, they are often used in a synthesis. Furthermore, most organic waste created by the chemical synthesis is attributable to organic solvents. Thus, an important issue is the use of alternative reaction media to overcome the problems associated with many of the traditional volatile organic solvents. It is believed that the best solvent is no solvent, or water [33]. Figure 1 shows the chemical structure of A-PEGCP. In this study, A-PEGCP is synthesized without using hazardous substances and any organic solvent at ambient pressure in a synthesis. Therefore, the synthesized processing has satisfied these principles [36] in this study.
Crystals 2020, 10, x FOR PEER REVIEW 3 of 11 substrates, and then annealed at different temperatures (80 °C, 100 °C, 120 °C and 140 °C, respectively) in N2 ambient for 1 h. Nanostructured properties of the thin films were examined by JEOL JEM-2100 TEM (Tokyo, Japan). PL spectra of the thin films were measured by a Hitachi F-4500 fluorescence spectrophotometer (Tokyo, Japan) and recorded in the range of 400-700 nm at 325 nm excitation wavelength at room temperature. UV-Vis absorption spectrum was measured by Shimadzu 3100 UV-Vis spectrophotometer (Tokyo, Japan) and employed to estimate the optical band-gap energy (Eg). UPS was measured by ULVAC-PHI PHI 5000 Versaprobe II (Kanagawa, Japan). Meanwhile, it was operated with He for photon energies of 21.2 eV and used to determine the binding energies of the highest occupied molecular orbital (HOMO) of the thin film. The thickness of the thin films was measured by surface profiler (Bruker Dektak XT) (Billerica, Massachusetts, USA). Meanwhile, the thickness of the thin films prepared from various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM) are 192 nm, 258 nm, 288 nm, 384 nm, and 1105 nm, respectively.

Results and Discussion
In general, organic solvents are volatile, flammable and toxic. However, they are often used in a synthesis. Furthermore, most organic waste created by the chemical synthesis is attributable to organic solvents. Thus, an important issue is the use of alternative reaction media to overcome the problems associated with many of the traditional volatile organic solvents. It is believed that the best solvent is no solvent, or water [33]. Figure 1 shows the chemical structure of A-PEGCP. In this study, A-PEGCP is synthesized without using hazardous substances and any organic solvent at ambient pressure in a synthesis. Therefore, the synthesized processing has satisfied these principles [36] in this study.  2 depicts PL spectra of the polymeric thin films prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM, respectively) and annealed at 140 °C. The PL peak of the polymeric thin film on ITO-coated glass is about 450 nm that extends from 360 to 650 nm. It also indicates that PL intensity of the polymeric thin film is concentration-dependent and increases with solution concentration. Traditional organic fluorescent materials that are composed of π-conjugated frameworks generally exhibit high-efficiency luminescence in diluted solution. Nevertheless, severe luminescence quenching of the fluorescent materials usually occurs in highly concentrated solutions or in the solid state because non-radiative pathways are formed in the short-range molecular interactions, such as π-π stacking originating from the planarity of the molecular skeleton. This phenomenon is known as aggregation-caused quenching (ACQ) [35]. In contrast, the result in Figure 2 suggests that the thin films prepared from A-PEGCP do not suffer from ACQ effect in this study. Generally, to maximize the performance of PLEDs, it is necessary for a polymeric thin film to avoid concentration quenching. From this point of view, the thin film prepared from A-PEGCP is appropriate for optoelectronic applications.  2 depicts PL spectra of the polymeric thin films prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM, respectively) and annealed at 140 • C. The PL peak of the polymeric thin film on ITO-coated glass is about 450 nm that extends from 360 to 650 nm. It also indicates that PL intensity of the polymeric thin film is concentration-dependent and increases with solution concentration. Traditional organic fluorescent materials that are composed of π-conjugated frameworks generally exhibit high-efficiency luminescence in diluted solution. Nevertheless, severe luminescence quenching of the fluorescent materials usually occurs in highly concentrated solutions or in the solid state because non-radiative pathways are formed in the short-range molecular interactions, such as π-π stacking originating from the planarity of the molecular skeleton. This phenomenon is known as aggregation-caused quenching (ACQ) [35]. In contrast, the result in Figure 2 suggests that the thin films prepared from A-PEGCP do not suffer from ACQ effect in this study. Generally, to maximize the performance of PLEDs, it is necessary for a polymeric thin film to avoid concentration quenching. From this point of view, the thin film prepared from A-PEGCP is appropriate for optoelectronic applications. On the other hand, the emission peak is gradually red-shifted from 447 to 461 nm when the concentration is changed from 1 to 50 mM. In other words, the PL peak shifts toward the longer wavelengths (a red shift) with increasing the concentration. It is generally suggested that the PL peak exhibits a blue shift with decreasing the size of nanostructure due to quantum confinement [37]. Accordingly, it is proposed that the diameter of the self-assembly nanoparticle decreases with decreasing the concentration in this study. That is, the higher the concentration of the A-PEGCP solution, the larger the size of the self-assembly nanoparticle. This can be attributed to the large amount of the polymers (higher concentration) that leads to larger self-assembly nanoparticle formation. Thus, PL peak exhibits a red shift as the concentration increases Figure 3 indicates UV-Vis absorption spectra of the polymeric thin films prepared from 1 to 50 mM solutions and annealed at 140 °C. It is observed that the spectra of the thin films are red-shifted with the concentration of the solution, indicating more molecular aggregation and stronger intermolecular interactions [38] in the polymeric thin film prepared from the higher concentrated solutions. That is, the higher the concentration, the more molecular aggregation. On the other hand, the most common technique for the determination of the optical band-gap energy (Eg) is optical absorption. An exciton is created by the absorption of a photon; the optical Eg is, therefore, derived from the onset of the optical absorption. The absorption onset is estimated by linear extrapolation of the low energy edge of the UV-Vis absorption spectrum. Consequently, as the concentrations of solutions are 1 mM, 5 mM, 10 mM, 25mM and 50 mM, the onset wavelengths (λonset) are 279 nm, 287 nm, 290 nm, 293 nm and 303 nm, respectively. The optical Eg is calculated using the formula Eg = 1240/λonset [39,40], here λonset is the onset wavelength. Thus, the optical Eg of the polymeric thin film prepared from 1 to 50 mM solution decreases from 4.44 to 4.09 eV. This result suggests that the optical Eg of the thin film decreases with increasing concentration. Although optical Eg is smaller than the true Eg because it does not take into account the exciton binding energy, it is generally used to estimate the difference between the highest occupied molecular orbital (HOMO) and the lowest unoccupied molecular orbital (LUMO) energy [41][42][43]. Thus it indicates that A-PEGCP with the wide Eg can be a promising candidate for a host material in PLED applications.  On the other hand, the emission peak is gradually red-shifted from 447 to 461 nm when the concentration is changed from 1 to 50 mM. In other words, the PL peak shifts toward the longer wavelengths (a red shift) with increasing the concentration. It is generally suggested that the PL peak exhibits a blue shift with decreasing the size of nanostructure due to quantum confinement [37]. Accordingly, it is proposed that the diameter of the self-assembly nanoparticle decreases with decreasing the concentration in this study. That is, the higher the concentration of the A-PEGCP solution, the larger the size of the self-assembly nanoparticle. This can be attributed to the large amount of the polymers (higher concentration) that leads to larger self-assembly nanoparticle formation. Thus, PL peak exhibits a red shift as the concentration increases. Figure 3 indicates UV-Vis absorption spectra of the polymeric thin films prepared from 1 to 50 mM solutions and annealed at 140 • C. It is observed that the spectra of the thin films are red-shifted with the concentration of the solution, indicating more molecular aggregation and stronger intermolecular interactions [38] in the polymeric thin film prepared from the higher concentrated solutions. That is, the higher the concentration, the more molecular aggregation. On the other hand, the most common technique for the determination of the optical band-gap energy (E g ) is optical absorption. An exciton is created by the absorption of a photon; the optical E g is, therefore, derived from the onset of the optical absorption. The absorption onset is estimated by linear extrapolation of the low energy edge of the UV-Vis absorption spectrum. Consequently, as the concentrations of solutions are 1 mM, 5 mM, 10 mM, 25 mM and 50 mM, the onset wavelengths (λ onset ) are 279 nm, 287 nm, 290 nm, 293 nm and 303 nm, respectively. The optical E g is calculated using the formula E g = 1240/λ onset [39,40], here λ onset is the onset wavelength. Thus, the optical E g of the polymeric thin film prepared from 1 to 50 mM solution decreases from 4.44 to 4.09 eV. This result suggests that the optical E g of the thin film decreases with increasing concentration. Although optical E g is smaller than the true E g because it does not take into account the exciton binding energy, it is generally used to estimate the difference between the highest occupied molecular orbital (HOMO) and the lowest unoccupied molecular orbital (LUMO) energy [41][42][43]. Thus it indicates that A-PEGCP with the wide E g can be a promising candidate for a host material in PLED applications.   Figure 4 illustrates the mean diameter of the self-assembly nanoparticle in the polymeric thin film prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM, respectively) and annealed at 140 °C. The size of the nanoparticle in the thin film is extracted from TEM image (in Figure S1). With an increasing concentration (from 1 to 50 mM), the average size of the nanoparticle increases from 3.7 ± 2.0 nm to 52.8 ± 8.3 nm. It has been proposed that the self-assembly nanoparticle is built of bisphenol-A aggregates and poly(ethylene glycol) moieties [34]. Therefore, the increase in the size of the nanoparticle with increasing concentration can be explained by the huge increase in the amount of bisphenol-A aggregates and poly(ethylene glycol) moieties in the higher concentrated solution. In other words, the larger amount (the higher concentration) of bisphenol-A aggregates and poly(ethylene glycol) moieties, the larger the diameter of the self-assembly nanoparticle. Accordingly, the results in Figure 4 are consistent with the results in Figures 2 and 3. Besides, the surface morphologies of the polymeric thin films prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM) are also shown in Figure S2.     Figure S1). With an increasing concentration (from 1 to 50 mM), the average size of the nanoparticle increases from 3.7 ± 2.0 nm to 52.8 ± 8.3 nm. It has been proposed that the self-assembly nanoparticle is built of bisphenol-A aggregates and poly(ethylene glycol) moieties [34]. Therefore, the increase in the size of the nanoparticle with increasing concentration can be explained by the huge increase in the amount of bisphenol-A aggregates and poly(ethylene glycol) moieties in the higher concentrated solution. In other words, the larger amount (the higher concentration) of bisphenol-A aggregates and poly(ethylene glycol) moieties, the larger the diameter of the self-assembly nanoparticle. Accordingly, the results in Figure 4 are consistent with the results in Figures 2 and 3. Besides, the surface morphologies of the polymeric thin films prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM) are also shown in Figure S2.  Figure 4 illustrates the mean diameter of the self-assembly nanoparticle in the polymeric thin film prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM, respectively) and annealed at 140 °C. The size of the nanoparticle in the thin film is extracted from TEM image (in Figure S1). With an increasing concentration (from 1 to 50 mM), the average size of the nanoparticle increases from 3.7 ± 2.0 nm to 52.8 ± 8.3 nm. It has been proposed that the self-assembly nanoparticle is built of bisphenol-A aggregates and poly(ethylene glycol) moieties [34]. Therefore, the increase in the size of the nanoparticle with increasing concentration can be explained by the huge increase in the amount of bisphenol-A aggregates and poly(ethylene glycol) moieties in the higher concentrated solution. In other words, the larger amount (the higher concentration) of bisphenol-A aggregates and poly(ethylene glycol) moieties, the larger the diameter of the self-assembly nanoparticle. Accordingly, the results in Figure 4 are consistent with the results in Figures 2 and 3. Besides, the surface morphologies of the polymeric thin films prepared by using various solutions (1 mM, 5 mM, 10 mM, 25 mM and 50 mM) are also shown in Figure S2.    Figure 5 reveals PL spectra of polymeric thin films prepared from 1 mM solution and annealed at different temperatures (80 • C, 100 • C, 120 • C and 140 • C, respectively). The PL intensity slightly decreases with annealing temperature. Moreover, the emission peak is slightly red-shifted from 436 to 441 nm as annealing temperature increases from 80 to 140 • C. It is deduced that during annealing, solvent evaporation leads to partial dissociation of the self-assembly nanoparticles and subsequent Crystals 2020, 10, 390 6 of 11 reconstruction of the self-assembly nanoparticles [44]. So, the higher annealing temperature enhances nanoparticle reformation. Hence the nanoparticle size increases slightly with increasing annealing temperature so that PL spectra are red-shifted with annealing temperature. It is, therefore, worth noting that annealing is a critical process in the fabrication of nanoparticle-based films [45].
Crystals 2020, 10, x FOR PEER REVIEW 6 of 11 decreases with annealing temperature. Moreover, the emission peak is slightly red-shifted from 436 to 441 nm as annealing temperature increases from 80 to 140 °C. It is deduced that during annealing, solvent evaporation leads to partial dissociation of the self-assembly nanoparticles and subsequent reconstruction of the self-assembly nanoparticles [44]. So, the higher annealing temperature enhances nanoparticle reformation. Hence the nanoparticle size increases slightly with increasing annealing temperature so that PL spectra are red-shifted with annealing temperature. It is, therefore, worth noting that annealing is a critical process in the fabrication of nanoparticle-based films [45].  The emission peak is red-shifted (5 nm) with increasing excitation wavelength (from 266 to 325 nm). Meanwhile, the EWDP phenomenon of A-PEGCP is not only observed in dichloromethane (CH2Cl2), but also in water. Therefore, EWDP behavior of A-PEGCP is found in both solid thin film and liquid states. So far, the EWDP property has been rarely observed in thin films. The EWDP phenomenon is generally observed in solutions and ascribed to a size distribution in nanostructures, solvation process in polar solvent, photo-enhanced oxygen adsorption, photo-corrosion process and the advancing of fast ionization processes under higher energy excitation [46]. In this study, while the concentrations of the solutions are 1 mM, 5 mM, 10 mM, 25 mM and 50 mM, the size distributions of the nanoparticles in thin films are in the ranges of 0.7-5.9 nm, 5.8-14.1 nm, 17.7-45.2 nm, 14.5-80 nm, and 15.3-61.2 nm, respectively. Thus, it is suggested that the EWDP phenomenon is attributed to a size distribution of self-assembly nanoparticles, where the PL emission is dependent on the size of the self-assembly nanoparticle due to the quantum size effect in this study.  The emission peak is red-shifted (5 nm) with increasing excitation wavelength (from 266 to 325 nm). Meanwhile, the EWDP phenomenon of A-PEGCP is not only observed in dichloromethane (CH 2 Cl 2 ), but also in water. Therefore, EWDP behavior of A-PEGCP is found in both solid thin film and liquid states. So far, the EWDP property has been rarely observed in thin films. The EWDP phenomenon is generally observed in solutions and ascribed to a size distribution in nanostructures, solvation process in polar solvent, photo-enhanced oxygen adsorption, photo-corrosion process and the advancing of fast ionization processes under higher energy excitation [46]. In this study, while the concentrations of the solutions are 1 mM, 5 mM, 10 mM, 25 mM and 50 mM, the size distributions of the nanoparticles in thin films are in the ranges of 0.7-5.9 nm, 5.8-14.1 nm, 17.7-45.2 nm, 14.5-80 nm, and 15.3-61.2 nm, respectively. Thus, it is suggested that the EWDP phenomenon is attributed to a size distribution of self-assembly nanoparticles, where the PL emission is dependent on the size of the self-assembly nanoparticle due to the quantum size effect in this study.  Figure 7 demonstrates PL spectra of the polymeric thin film prepared from 1 mM solution and annealed at 140 °C as deposited and prepared after seven months. It clearly shows that the PL intensity decreases with time. It is proposed that oxygen diffuses into the polymer from air and quenches the PL of the polymer to an extent that depends on the amount of oxygen present in the polymeric film [47,48]. Furthermore, the result also shows that the position of the PL emission peak is red-shifted with time. This red shift amounts to 14 nm. It is deduced that localized shallow traps are formed in the band-tail states in the surface of the thin film due to the exposure to moisture without encapsulation [49]. These shallow trap states, energy levels close to HOMO and LUMO energy levels, can act as radiative recombination channels and emit photons with less energy than those related with the LUMO-to-HOMO transition, leading to a red shift in PL spectra.    Figure 7 demonstrates PL spectra of the polymeric thin film prepared from 1 mM solution and annealed at 140 • C as deposited and prepared after seven months. It clearly shows that the PL intensity decreases with time. It is proposed that oxygen diffuses into the polymer from air and quenches the PL of the polymer to an extent that depends on the amount of oxygen present in the polymeric film [47,48]. Furthermore, the result also shows that the position of the PL emission peak is red-shifted with time. This red shift amounts to 14 nm. It is deduced that localized shallow traps are formed in the band-tail states in the surface of the thin film due to the exposure to moisture without encapsulation [49]. These shallow trap states, energy levels close to HOMO and LUMO energy levels, can act as radiative recombination channels and emit photons with less energy than those related with the LUMO-to-HOMO transition, leading to a red shift in PL spectra.  Figure 7 demonstrates PL spectra of the polymeric thin film prepared from 1 mM solution and annealed at 140 °C as deposited and prepared after seven months. It clearly shows that the PL intensity decreases with time. It is proposed that oxygen diffuses into the polymer from air and quenches the PL of the polymer to an extent that depends on the amount of oxygen present in the polymeric film [47,48]. Furthermore, the result also shows that the position of the PL emission peak is red-shifted with time. This red shift amounts to 14 nm. It is deduced that localized shallow traps are formed in the band-tail states in the surface of the thin film due to the exposure to moisture without encapsulation [49]. These shallow trap states, energy levels close to HOMO and LUMO energy levels, can act as radiative recombination channels and emit photons with less energy than those related with the LUMO-to-HOMO transition, leading to a red shift in PL spectra.    Figure 8 presents the UPS spectrum of the polymeric thin film prepared from 10 mM solution and annealed at 140 • C on Au-coated Si substrate. UPS is based on the photoelectric effect. UPS probes the energy of the occupied levels by using ultraviolet radiation. The ionization energy is determined by linearly extrapolating the high and low energy slopes of the spectrum to the spectral base lines. The HOMO position relative to the vacuum level is estimated by linearly extrapolating the low and high binding energy side of the spectrum to the base lines. That is, the intersection of the lines at high binding energy provides an estimate of the lowest energy electrons. The difference between the two energies is the maximum of the kinetic energy, E kin , of the emitted HOMO electrons at the surface of the low and high binding energy side of the spectrum to the base lines. That is, the intersection of the lines at high binding energy provides an estimate of the lowest energy electrons. The difference between the two energies is the maximum of the kinetic energy, Ekin, of the emitted HOMO electrons at the surface of the thin film, so HOMO energy is calculated from HOMO energy = Ekin -21.2 eV [50,51]. Thus HOMO energy of the thin film prepared from A-PEGCP is estimated about -9.52 eV.

Conclusions
Thin films prepared from A-PEGCP with self-assembly nanoparticles that have been spin-coated on ITO-coated glass substrates are smooth and uniform. The TEM images demonstrate nanoparticles are formed with a mean diameter distribution ranging from 3.7 to 52.8 nm as the concentration increases from 1 to 50 mM. It is suggested that the increase in the size of the nanoparticle with increasing concentration can be ascribed to the enormous increase in the amount of bisphenol-A aggregates and poly(ethylene glycol) moieties in the higher concentrated solution. In addition, PL intensity increases with concentration. Thus, it clearly shows that there is no ACQ effect in the thin films. Meanwhile, PL spectra present a slight red shift (14 nm) with increasing concentrations from 1 to 50 mM. The UV-Vis absorption spectra of the thin films are also red-shifted with concentration, indicating more molecular aggregation and stronger intermolecular interactions in the thin films prepared from higher concentrated solutions. Furthermore, PL intensity slightly decreases with annealing temperature. Meanwhile, PL spectra also show a slight red shift (5 nm) with increasing annealing temperature from 80 to 140 ºC. It is proposed that the higher annealing temperature enhances the reconstruction of the self-assembly nanoparticles. The polymeric thin film exhibits the EWDP property with PL peaks ranging from 446 to 451 nm under excitation from 266 to 325 nm. It is, therefore, suggested that EWDP behavior is ascribed to a nearly continuous size distribution of nanoparticles. Moreover, it is proposed that oxygen diffuses into the thin film from air and quenches the PL of the thin film. Meanwhile, the red shift of PL spectra with aging is attributed to localized shallow traps induced by moisture without encapsulation. Consequently, optical properties of polymeric thin films with self-assembly nanoparticles are influenced by concentration, thermal annealing, nanoparticle size and moisture. Besides, HOMO energy is obtained of about -9.52 eV. The optical band gap is 4.09-4.44 eV. These results illustrate that the thin film with self-assembly nanoparticles is a promising candidate for a host material in PLED applications.

Conclusions
Thin films prepared from A-PEGCP with self-assembly nanoparticles that have been spin-coated on ITO-coated glass substrates are smooth and uniform. The TEM images demonstrate nanoparticles are formed with a mean diameter distribution ranging from 3.7 to 52.8 nm as the concentration increases from 1 to 50 mM. It is suggested that the increase in the size of the nanoparticle with increasing concentration can be ascribed to the enormous increase in the amount of bisphenol-A aggregates and poly(ethylene glycol) moieties in the higher concentrated solution. In addition, PL intensity increases with concentration. Thus, it clearly shows that there is no ACQ effect in the thin films. Meanwhile, PL spectra present a slight red shift (14 nm) with increasing concentrations from 1 to 50 mM. The UV-Vis absorption spectra of the thin films are also red-shifted with concentration, indicating more molecular aggregation and stronger intermolecular interactions in the thin films prepared from higher concentrated solutions. Furthermore, PL intensity slightly decreases with annealing temperature. Meanwhile, PL spectra also show a slight red shift (5 nm) with increasing annealing temperature from 80 to 140 ºC. It is proposed that the higher annealing temperature enhances the reconstruction of the self-assembly nanoparticles. The polymeric thin film exhibits the EWDP property with PL peaks ranging from 446 to 451 nm under excitation from 266 to 325 nm. It is, therefore, suggested that EWDP behavior is ascribed to a nearly continuous size distribution of nanoparticles. Moreover, it is proposed that oxygen diffuses into the thin film from air and quenches the PL of the thin film. Meanwhile, the red shift of PL spectra with aging is attributed to localized shallow traps induced by moisture without encapsulation. Consequently, optical properties of polymeric thin films with self-assembly nanoparticles are influenced by concentration, thermal annealing, nanoparticle size and moisture. Besides, HOMO energy is obtained of about −9.52 eV. The optical band gap is 4.09-4.44 eV. These results illustrate that the thin film with self-assembly nanoparticles is a promising candidate for a host material in PLED applications.
Supplementary Materials: The following are available online at http://www.mdpi.com/2073-4352/10/5/390/s1, Figure S1: TEM images of the self-assembly nanoparticles prepared from different concentration solutions (from 1 to 50 mM); Figure S2: the surface morphologies of the polymeric thin films prepared from different concentration solutions (from 1 to 50 mM).