Synthesis of π-Conjugated Polymers Containing Benzotriazole Units via Palladium-Catalyzed Direct C-H Cross-Coupling Polycondensation for OLEDs Applications

Four D-π-A conjugated polymers, namely P1–P4, which contain benzotriazole building blocks in their backbone as acceptor, are synthesized via palladium-catalyzed direct C-H cross-coupling polycondensation of 5,6-difluorobenzotriazole with different thiophene derivatives, including 3-octylthiophene, 2,2’-bithiophene, thieno[3,4-b][1,4]dioxine, and 4,4-dioctyl-4H-silolo-[3,2-b:4,5-b’]dithiophene as donor units, respectively. Taking the polymer P1 as an example, the chemical structure of the polymer is demonstrated by 1H and 19F NMR spectra. The optical, electrochemical, and thermal properties of these polymers are assessed by UV–vis absorption and fluorescence spectroscopy, cyclic voltammetry (CV), and thermal gravimetric analysis (TGA), respectively. DFT simulations of all polymers are also performed to understand their physicochemical properties. Furthermore, P1 and P2, which have relatively higher molecular weights and better fluorescent quantum efficiency than those of P3 and P4, are utilized as lighting emitters for organic light-emitting diodes (OLEDs), affording promising green and red luminescence with 0.07% and 0.14% of maximum external quantum efficiency, respectively, based on a device with an architecture of ITO/PEDOT:PSS/PTAA/the polymer emitting layer/TPBi/LiF/Al.


Introduction
Organic light-emitting diodes (OLEDs) have received much attention both in academia and industry owing to their wide applications in fullcolor displays and solid-state lighting. π-Conjugated polymers have many unique photophysical properties that are inherited from the delocalized electronic structures of their backbones and, thus, they exhibit promising advantages, such as solution-processing, light-weight, low-cost, and facile preparation of flexible devices in various functional applications, such as OLEDs, solar cells, field-effect transistors (FETs), photodetectors, etc. [1][2][3][4][5][6].

Instruments
1 H and 13 C NMR spectra of polymers were measured on a Bruker AV400 at 25 • C utilizing the residual solvent peak as reference. Molecular weights of polymers were determined by gel permeation chromatography (GPC) on Waters 1525 equipped with Waters Styragel HT gel columns using tetrahydrofuran (THF) as eluent at 35 • C and monodisperse polystyrene as standard. Thermogravimetric analyses (TGA) were carried out on a Frontier Mid-IR FTIR/STA6000-TL9000-Clarus SQ8 instrument with a 10 • C·min −1 heating rate under a purified nitrogen gas flow. Optical properties of polymers including UV-vis absorption and photoluminescence (PL) spectra were obtained on a Shimadzu UV-2550 and Hitachi F-4600, respectively. Solid-state samples for the test of photophysical property were prepared by spin-casting of polymers chloroform solutions on quartz plates. Optical bandgaps were calculated based on the onset of the absorption spectra of the thin film. Cyclic voltammetry (CV) measurements are carried out on a LK98B II electrochemical analyzer at room temperature with the scan rate was 100 mV s −1 . In this experiment, a conventional three-electrode configuration was adopted, i.e., a glassy carbon electrode as the working electrode, a saturated calomel electrode (SCE) as the reference electrode, and a Pt wire as the counter electrode. Acetonitrile, freshly prepared (CH 3 CN) by distilling from calcium hydride (CaH) under dry N 2 , was used as solvent. Tetrabutylammonium phosphorus hexafluoride (Bu 4 NPF 6 ) with a concentration of 0.1 M in CH 3 CN was applied as the support electrolyte.

Device Fabrication and Characterization
The OLED devices with P1 and P2 as a light-emitting layer were fabricated with the following configuration: ITO/PSS:PEDOT/PTAA/polymer light-emitting layer/TPBi/LiF/Al.
In this experiment, indium tin oxide (ITO) glass with a conductivity of 10 Ω/square was first pre-cleaned with acetone and ethanol under ultrasound and was subsequently treated in an ultraviolet-ozone chamber. A thin 40 nm-thick PSS-PEDOT layer was spincoated onto the treated ITO glass which was placed on a hot plate at 3000 rpm for 10 min at 110 • C. The coated ITO glass was then transferred to a glovebox filled with N 2 and re-dried for 10 min at 110 • C. The solution of PTAA (5 mg) in 1 mL of DMF was then spin-coated onto the top of PSS:PEDOT layer on ITO to form an electron blocking layer with a thickness of 30 nm. After the above substrate was baked for 20 min at 100 • C, the toluene solution of P1 or P2 (10 mg/mL) was spin-coated onto PTAA layer to form a uniform 40 nm-thick light-emitting layer, which was followed by an annealing treatment for 10 min at 90 • C. Finally, using conventional thermal evaporation under vacuum, TPBi, LiF, and Al were deposited onto the surface of the active layer in sequence with the thicknesses of 30, 1, and 120 nm, respectively. The devices provided an active area of 5 × 3 mm 2 . Based on the above devices, the electroluminescence (EL) spectra, current density-voltage (J-V) and luminance-voltage (L-V) were obtained on a Keithley 2400 Source Meter system. The luminance of OLEDs was measured with a PhotoResearch SpectraScan PR-650 Colorimeter.
The polycondensation of 5,6-difluoro-2-(2-hexyldecyl)-2H-benzotriazole (1) with 3-octylthiophene provides the polymer P1 with an average molecular weight of M n = 22,300 in an excellent yield (93%). In the case of 2,2'-bithiophene as donor units, P2 with the highest molecular weight of M n = 28,100 was obtained in a good yield (82%). By contrast, the polymerization reaction of 1 with thieno[3,4-b] [1,4]dioxine mainly yielded an insoluble solid in common organic solvents, and only a small number of products can be isolated by Soxhlet extractions with CHCl 3 to provide a total yield of about 10%. This result may be due to the cross-linking reaction in multiple C-H systems [30,31]. Dithienosilole cores are common building blocks of various active materials used in photovoltaics, FETs, and OLEDs, etc. [32][33][34][35][36] because of their strong donating electron ability, photostability, and chemical stability. Under the same reaction conditions as that for P1-P3, the polycondensation of 1 with 4,4-dioctyl-4Hsilolo-[3,2-b:4,5-b']dithiophene yields a soluble polymer P4 in CHCl 3 with low yield (about 20%) ( Table 1, entry 4), which is similar to the case of P3. Most of the as-prepared polymers exhibit good thermal stability with the degradation temperatures at 5% weight loss are 385, 317, and 392 • C for P1, P2, and P4, respectively (Table 1), which is suitable for the applications in the semiconductor devices.

Structural Characterization
The chemical structure of polymers was determined by 1 H and 19 F NMR spectra ( Figure 1 and Figures S1-S8). Taking P1 as an example, all characteristic proton peaks corre- sponding to the benzotriazole and thiophene units can be observed as shown in Figure 1A, which is similar to the analogous polymers obtained via the Kumada method except for different alkyl side chains as reported by Bielawski and co-workers [10]. As seen in Figure 1A, the multiple peaks at 4.60-4.76 ppm (a in Figure 1A) and the broad peak at 2.28 ppm (b in Figure 1A) were assigned to the -CH 2 groups close to the triazole ring and -CH signal of the branched groups, respectively. The peak at 2.70 nm (c in Figure 1A) corresponds to -CH 2 groups of thiophene side chains. It was noted that the signal of aromatic hydrogen of thiophene units (d in Figure 1A) significantly shifted to low field compared with the corresponding thiophene monomer, which was possibly caused by F· · · H noncovalent interaction between the fluorine atoms on benzotriazole unit and the hydrogen atoms on thiophene units as demonstrated by our recent work [29] and the literature [11].
Most of the as-prepared polymers exhibit good thermal stability with the degradation temperatures at 5% weight loss are 385, 317, and 392 °C for P1, P2, and P4, respectively (Table 1), which is suitable for the applications in the semiconductor devices.

Structural Characterization
The chemical structure of polymers was determined by 1 H and 19 F NMR spectra (Figure 1 and Figures S1-S8). Taking P1 as an example, all characteristic proton peaks corresponding to the benzotriazole and thiophene units can be observed as shown in Figure  1A, which is similar to the analogous polymers obtained via the Kumada method except for different alkyl side chains as reported by Bielawski and co-workers [10]. As seen in Figure 1A, the multiple peaks at 4.60-4.76 ppm (a in Figure 1A) and the broad peak at 2.28 ppm (b in Figure 1A) were assigned to the -CH2 groups close to the triazole ring and -CH signal of the branched groups, respectively. The peak at 2.70 nm (c in Figure 1A) corresponds to -CH2 groups of thiophene side chains. It was noted that the signal of aromatic hydrogen of thiophene units (d in Figure 1A) significantly shifted to low field compared with the corresponding thiophene monomer, which was possibly caused by F⋯H noncovalent interaction between the fluorine atoms on benzotriazole unit and the hydrogen atoms on thiophene units as demonstrated by our recent work [29] and the literature [11]. Besides, 19 F NMR was also applied to confirm the polymers' chemical structure since it has many merits, including high sensitivity, little interference, a large range of chemical Besides, 19 F NMR was also applied to confirm the polymers' chemical structure since it has many merits, including high sensitivity, little interference, a large range of chemical shifts, and similar structures that are not easy to overlap, etc. As depicted in Figure 1B, the 19 F NMR of P1 displayed an obvious main peak at −133.0 ppm that corresponds to the fluorine atoms on the polymeric chains. The remaining weak signals could be assigned to the end groups, where the fluorine atoms are not chemically equivalent to those along the backbone [37]. All the NMR results of P1 suggest an alternating structure along the polymer main chain.

DFT Simulation
Density functional theory (DFT) simulation was performed at the B3LYP/6-31G* level using Gaussian 09 programs to check the effect of the structure of thiophene donor units on the polymer backbone on the HOMO and LUMO energy levels of the resultant polymers. In this study, four repeated D-A units were used and all side chains were replaced with methyl groups to simplify the calculation. The HOMO and LUMO level values were obtained by MO topologies on the basis of the optimized geometry. As shown in Figure 2 which is beneficial to charge-carrier transport. Thus, these polymers were suitable for active materials of OLED devices. Additionally, it can be clearly seen from the molecular orbital diagrams that the HOMO energy levels of the four polymers all remain delocalized along the main chain of polymers, and the HOMO energy levels of P1-P4 are −4.74, −4.71, −4.72, and −4.47 eV, respectively. While the electron density is successively distributed on the whole D-A units, the LUMO values of P1-P4 are calculated to be −2.61, −2.64, −1.98, and −2.47 eV, respectively. It is important to note that the thiophene segments tend to be trans-coplanar with benzotriazole units in the optimized geometries of P1 (Figure 2), where the sulfur atom of the thiophene unit is in the opposite position to the fluorine atom of the thiazole unit. This conformation is undoubtedly conducive to the formation of F· · · H non-covalent interactions as demonstrated by 1 H NMR spectra shown in Figure 1A.
Density functional theory (DFT) simulation was performed at the B3LYP/6-31G* level using Gaussian 09 programs to check the effect of the structure of thiophene donor units on the polymer backbone on the HOMO and LUMO energy levels of the resultant polymers. In this study, four repeated D-A units were used and all side chains were replaced with methyl groups to simplify the calculation. The HOMO and LUMO level values were obtained by MO topologies on the basis of the optimized geometry. As shown in Figure  2, the contour plots indicated the effective separation of HOMO and LUMO levels for all polymers P1-P4, which is beneficial to charge-carrier transport. Thus, these polymers were suitable for active materials of OLED devices. Additionally, it can be clearly seen from the molecular orbital diagrams that the HOMO energy levels of the four polymers all remain delocalized along the main chain of polymers, and the HOMO energy levels of P1-P4 are −4.74, −4.71, −4.72, and −4.47 eV, respectively. While the electron density is successively distributed on the whole D-A units, the LUMO values of P1-P4 are calculated to be −2.61, −2.64, −1.98, and −2.47 eV, respectively. It is important to note that the thiophene segments tend to be trans-coplanar with benzotriazole units in the optimized geometries of P1 (Figure 2), where the sulfur atom of the thiophene unit is in the opposite position to the fluorine atom of the thiazole unit. This conformation is undoubtedly conducive to the formation of F⋯H non-covalent interactions as demonstrated by 1 H NMR spectra shown in Figure 1A.

UV-vis Absorption Spectra
The UV-vis absorption spectra of P1-P4 in dilute chloroform (CHCl 3 ) solutions and in film states were measured on a Shimadzu UV-2550 spectrometer. The concentration of the polymer in CHCl 3 solution was 10 −5 mol/L based on repeated units. The film samples were prepared by casting the chloroform solutions (3 mg/mL) on the surface of quartz and subsequently annealing for 10 min at 100 • C. Their UV-vis absorption spectra of polymer solutions and thin films are presented in Figure 3, and the absorption maxima and the optical band gaps estimated from the absorption edge of the thin film are listed in Table 2. in film states were measured on a Shimadzu UV-2550 spectrometer. The concentration of the polymer in CHCl3 solution was 10 −5 mol/L based on repeated units. The film samples were prepared by casting the chloroform solutions (3 mg/mL) on the surface of quartz and subsequently annealing for 10 min at 100 °C. Their UV-vis absorption spectra of polymer solutions and thin films are presented in Figure 3, and the absorption maxima and the optical band gaps estimated from the absorption edge of the thin film are listed in Table  2.  As shown in Figure 3a and Table 2, the λmax of P1-P4 in CHCl3 solutions are 427, 515, 471, and 506 nm, respectively. Compared with P1, a remarkable redshift by 88 nm was observed for P2 in CHCl3 solutions, possibly due to P2 having longer conjugated chains and a more efficient conjugated effect caused by smaller steric hindrance between benzotriazole units and dithiophene units. In addition, the λmax of all polymers in the thin film states exhibit negligible changes in comparison with that in solutions beside P4. The results should be attributed to only P4 tending to form a more coplanar configuration between benzotriazole segments and silole ring in the solid-state due to the completely symmetrical and rigidly planar structure of silole units as demonstrated by DFT calculation (Figure 2). The optical band gaps (Eg opt ) of P1-P4 were determined to be 2.16, 1.81, 1.85, and 1.88 eV, respectively, from the onsets of the spectra in the films. The results are close  As shown in Figure 3a and Table 2, the λ max of P1-P4 in CHCl 3 solutions are 427, 515, 471, and 506 nm, respectively. Compared with P1, a remarkable redshift by 88 nm was observed for P2 in CHCl 3 solutions, possibly due to P2 having longer conjugated chains and a more efficient conjugated effect caused by smaller steric hindrance between benzotriazole units and dithiophene units. In addition, the λ max of all polymers in the thin film states exhibit negligible changes in comparison with that in solutions beside P4. The results should be attributed to only P4 tending to form a more coplanar configuration between benzotriazole segments and silole ring in the solid-state due to the completely symmetrical and rigidly planar structure of silole units as demonstrated by DFT calculation (Figure 2). The optical band gaps (E g opt ) of P1-P4 were determined to be 2.16, 1.81, 1.85, and 1.88 eV, respectively, from the onsets of the spectra in the films. The results are close to the corresponding E g opt values of the other benzotriazole-based D-π-A conjugated polymers reported in the literature, including ours [9,27]. Figure 4a shows the photoluminescence (PL) spectra in CHCl 3 solutions. P1-P4 exhibit broad emission peaks in the range of 480-770 nm upon excitation at 420 nm. In the case of P2 and P4, the obvious shoulder bands at about 630 nm could be attributed to the intramolecular charge transfer (ICT) from thiophene units to benzotriazole units (Figure 4a) [38,39]. Additionally, it was noted that emission peaks of polymers vary with the different donor units, exhibiting a bathochromic displacement observed in the following order: P1 < P3 < P2 ≈ P4 (Figure 4a). Thus, the polymers P2 and P4 with the more extended conjugated backbones show the maximum emission peaks at the highest wavelengths between 550 and 650 nm (Figure 4a). case of P2 and P4, the obvious shoulder bands at about 630 nm could be attributed to the intramolecular charge transfer (ICT) from thiophene units to benzotriazole units ( Figure  4a) [38,39]. Additionally, it was noted that emission peaks of polymers vary with the different donor units, exhibiting a bathochromic displacement observed in the following order: P1 < P3 < P2 ≈ P4 (Figure 4a). Thus, the polymers P2 and P4 with the more extended conjugated backbones show the maximum emission peaks at the highest wavelengths between 550 and 650 nm (Figure 4a). Different emission behavior of the polymers was noticed in solid-state. P1 maintained a similar emission profile to that in solution but consisted of a larger spectral domain, extended to most of the visible light region from 500 to 700 nm. The solid-state P2 displayed a very wide emission extended into the near-infrared domain, with an emission peak located at near 700 nm (Figure 4b). Compared with the emission peak of P2 in solution, its significant red-shift in thin-film state was noted. This should be attributed to more effective conjugation of polymer chains due to the intramolecular rotation that was restricted in solid-state. For the films of P3 and P4, only very weak emissions were observed (not provided), which agrees with the results of similar polymers reported in the literature [40].

Electrochemical Property
The electrochemical properties of all polymers P1-P4 were assessed by standard cyclic voltammetry (CV) using a saturated calomel electrode as reference electrode and the energy level of ferrocene/ferrocenium (−4.80 eV) as the internal standard (Figures S10 and S11). The energy levels of P1-P4, calculated on the basis of CV curves, are presented in Table 2. The HOMO levels of P1-P4 are −5.57, −5.69, −5.45, and −5.67 eV, respectively versus Fc/Fc + , and obviously lower than that of classical poly(3-hexylthiophene) (P3HT) materials (−5.10 eV) [41]. The results also indicate that the HOMO levels of benzotriazolebased conjugated polymers can be finely tuned by the introduction of different donor units. After magnification of the CV plots, the onsets of reduction potentials (Eonset red ) could be determined to be −0.73, −0.81, −0.82, and −0.83 V for P1-P4, respectively. Hence, the Different emission behavior of the polymers was noticed in solid-state. P1 maintained a similar emission profile to that in solution but consisted of a larger spectral domain, extended to most of the visible light region from 500 to 700 nm. The solid-state P2 displayed a very wide emission extended into the near-infrared domain, with an emission peak located at near 700 nm (Figure 4b). Compared with the emission peak of P2 in solution, its significant red-shift in thin-film state was noted. This should be attributed to more effective conjugation of polymer chains due to the intramolecular rotation that was restricted in solid-state. For the films of P3 and P4, only very weak emissions were observed (not provided), which agrees with the results of similar polymers reported in the literature [40].

Electrochemical Property
The electrochemical properties of all polymers P1-P4 were assessed by standard cyclic voltammetry (CV) using a saturated calomel electrode as reference electrode and the energy level of ferrocene/ferrocenium (−4.80 eV) as the internal standard ( Figures S10 and S11). The energy levels of P1-P4, calculated on the basis of CV curves, are presented in Table 2. The HOMO levels of P1-P4 are −5.57, −5.69, −5.45, and −5.67 eV, respectively versus Fc/Fc + , and obviously lower than that of classical poly(3-hexylthiophene) (P3HT) materials (−5.10 eV) [41]. The results also indicate that the HOMO levels of benzotriazole-based conjugated polymers can be finely tuned by the introduction of different donor units. After magnification of the CV plots, the onsets of reduction potentials (E onset red ) could be determined to be −0.73, −0.81, −0.82, and −0.83 V for P1-P4, respectively. Hence, the LUMO energy levels of polymers P1-P4 can be obtained to be −3.60, −3.68, −3.59, and −3.58 eV, respectively, versus Fc/Fc + according to the corresponding E onset red . Since the conjugated polymers containing fluorinated benzotriazole segments can display excellent oxidational stability due to the stabilized HOMO and LUMO levels by the strong inductive effect of fluorine atoms [11,42], such polymer materials should have a huge potential for application in various photoelectric devices.

Electroluminescence Characteristics
Considering that P1 and P2 have relatively high M n and good fluorescent quantum efficiency in solutions (η = 0.3837 and 0.3805 for P1 and P2, respectively, measured on a FLS1000 fluorescence spectrometer, Edinburgh, UK), the solution-processed OLED devices with the P1 and P2 as emissive layers were fabricated based on the following configuration: ITO/PEDOT:PSS/PTAA/emissive layer/TPBi/LiF/Al. Figure 5 shows the electroluminescent (EL) spectra of the devices with the P1 and P2 as the emissive layer, respectively. The emission maxima of P1 and P2-based EL devices were 544 and 640 nm, respectively, which Polymers 2021, 13, 254 9 of 12 were slightly blue-shifted in comparison with the corresponding photoluminescence ones in the solid films as shown in Figure 4b. These results suggest that the color tuning on the EL device of benzotriazole-based polymers through the incorporation of various donor units on their backbone is feasible.
Considering that P1 and P2 have relatively high Mn and good fluorescent quantum efficiency in solutions (η = 0.3837 and 0.3805 for P1 and P2, respectively, measured on a FLS1000 fluorescence spectrometer, Edinburgh, UK), the solution-processed OLED devices with the P1 and P2 as emissive layers were fabricated based on the following configuration: ITO/PEDOT:PSS/PTAA/emissive layer/TPBi/LiF/Al. Figure 5 shows the electroluminescent (EL) spectra of the devices with the P1 and P2 as the emissive layer, respectively. The emission maxima of P1 and P2-based EL devices were 544 and 640 nm, respectively, which were slightly blue-shifted in comparison with the corresponding photoluminescence ones in the solid films as shown in Figure 4b. These results suggest that the color tuning on the EL device of benzotriazole-based polymers through the incorporation of various donor units on their backbone is feasible. Figure 5. EL spectra P1 and P2-based devices. Figure 6 shows the typical EL performances of P1 and P2-based devices and their EL characteristics that were also listed in Table 3. The rectification behavior of P1 and P2based devices can be observed from their J-V curves ( Figure S12) originating from the intrinsic properties of the diodes. The turn-on voltages (Von) of P1-and P2-based devices were 4.0 and 3.0 V, respectively, as shown in Figure 6a. The P2-based device provided a higher luminance and current efficiency than that of P1 at a certain bias, as shown in Figure 6a,b. As a result, the maximum power efficiency (ηp = 0.13 lm/W) and the maximum external quantum efficiency (EQEmax = 0.14%) for P2-based OLED devices, which is almost twice as much as that for P1-based devices (Figure 6c,d). The P1-based device exhibited a bright green emission with CIE coordinates of (0.40, 0.52) (Figure 6e), while a red emission with CIE coordinates of (0.66, 0.33) at 1200 cd/m 2 was observed for P2-based devices (Figure 6f). This result indicates P2 is a promising red emissive material for OLEDs.  Figure 6 shows the typical EL performances of P1 and P2-based devices and their EL characteristics that were also listed in Table 3. The rectification behavior of P1 and P2-based devices can be observed from their J-V curves ( Figure S12) originating from the intrinsic properties of the diodes. The turn-on voltages (V on ) of P1-and P2-based devices were 4.0 and 3.0 V, respectively, as shown in Figure 6a. The P2-based device provided a higher luminance and current efficiency than that of P1 at a certain bias, as shown in Figure 6a,b. As a result, the maximum power efficiency (η p = 0.13 lm/W) and the maximum external quantum efficiency (EQE max = 0.14%) for P2-based OLED devices, which is almost twice as much as that for P1-based devices (Figure 6c,d). The P1-based device exhibited a bright green emission with CIE coordinates of (0.40, 0.52) (Figure 6e), while a red emission with CIE coordinates of (0.66, 0.33) at 1200 cd/m 2 was observed for P2-based devices (Figure 6f). This result indicates P2 is a promising red emissive material for OLEDs.

Conclusions
Four benzotriazole-based π-conjugated polymers with donor-acceptor alternating structure were successfully prepared via Pd-catalyzed direct C-H cross-coupling polycondensation. The protocol offers a straightforward and effective assessment of such polymers without any pre-functionalized steps. This work extends the range of aromatic monomers for direct C-H cross-coupling polycondensation and achieves the effective copolymerization of electron-deficient benzotriazole with electron-rich thiophene derivatives in a structurally controllable mode. Although the as-synthesized polymer materials only displayed moderate OLED performances, the present method could have enormous potential for the synthesis of various semiconducting materials by tuning donor and acceptor units for different organic optoelectronic device applications.

Conclusions
Four benzotriazole-based π-conjugated polymers with donor-acceptor alternating structure were successfully prepared via Pd-catalyzed direct C-H cross-coupling polycondensation. The protocol offers a straightforward and effective assessment of such polymers without any pre-functionalized steps. This work extends the range of aromatic monomers for direct C-H cross-coupling polycondensation and achieves the effective copolymerization of electron-deficient benzotriazole with electron-rich thiophene derivatives in a structurally controllable mode. Although the as-synthesized polymer materials only displayed moderate OLED performances, the present method could have enormous potential for the synthesis of various semiconducting materials by tuning donor and acceptor units for different organic optoelectronic device applications.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.