Vertical Alignment of Liquid Crystals on Phenylphenoxymethyl-Substituted Polystyrene—PS Derivatives Structurally Similar to LC Molecules

A series of polystyrene derivatives containing precursors of liquid crystal (LC) molecules, phenylphenoxymethyl-substituted polystyrene (PPHE#; # = 5, 15, 25, 50, 75, and 100)—where # is the molar content of 4-phenylphenol using polymer modification reactions—were prepared in order to examine the effect of the polymer film, which possess similar LC molecular structure on the LC alignment properties. It was found that the Tg values of the PPHE# were higher than 100 °C due to their aromatic structure in the biphenyl-based PHE moiety. The LC cells fabricated with PPHE5 and PPHE15 films exhibited planar LC alignment. Conversely, LC molecules showed a vertical alignment in LC cells made using the polymer films with phenylphenoxymethyl side groups in the range of 25–100 mol %. The polar surface energies on the PPHE# films can be associated with the vertical LC alignment on the PPHE# films. For example, vertical LC alignment was exhibited when the polar surface energy of the polymer films was less than approximately 4.2 mJ/m2. Aligning stability was observed at 200 °C and UV irradiation of 20 J/cm2 for LC cells made using the PPHE100 film. Therefore, it was found that biphenyl, one of the LC precursors, modified polystyrene derivatives and can produce a next-generation vertical LC alignment system.


Introduction
The physicochemical properties-such as thermal conductivity [1][2][3][4], mechanical properties [5][6][7], and wettability [8,9]-of anisotropic molecules are influenced by their molecular alignments. For example, the thermal conductivity of anisotropic molecules could be changed by adjusting the molecular orientation in the polymer chain. The polymer chains oriented parallel with regard to the direction of heat transfer are preferred for enhancing thermal conductivity because carbon-carbon covalent bonds transport atomic thermal vibrational energy compared to van der Waals interactions between polymer interchains [1,2]. The thermal conductivity of polyethylene in parallel with regard to the polymer chain is considerably larger than polyethylene which is perpendicular with regard to the polymer chain, due to the aforementioned mechanism [10]. The mechanical properties are also associated with the alignment of anisotropic molecules. The tensile strength of materials containing anisotropic molecules oriented in parallel to the applied load is larger than that containing anisotropic molecules with a perpendicular orientation with respect to the applied load. For instance, polymer reinforced with glass fiber exhibits interesting mechanical properties according to orientation of the glass fiber. The maximum tensile strength of the polymer samples was observed for glass fiber oriented in parallel with respect to the external stress [5][6][7]. In addition, the surface properties of polymeric materials could be controlled by the implementation of anisotropic characteristics onto the polymeric surface. For example, polydimethylsiloxane (PDMS) is restricted to biomedical applications such as biosensors and implants, owing to the hydrophobic characteristics can induce the vertical alignment of LC molecules. The surface energy value of polymer films and the molecular alignment in the polymer chains are crucial factors in producing vertical LC alignment behavior due to the interactions and/or steric repulsions between polymer surfaces and LC molecules [61,62].
In this article, a series of phenylphenoxymethyl-substituted polystyrene (PPHE#) derivatives having an aromatic structure in the biphenyl-based moiety was synthesized to investigate LC behaviors on the alignment film made from PS derivatives structurally similar to LC molecules. This study suggests that the structural similarity between the LC molecules and alignment layer can be favorable in the vertical alignment of LC molecules. We could vary the molar content of the phenylphenoxymethyl group, and the effect of biphenyl moiety, a representative of an LC building block, in the side chain on their LC alignment behaviors could be studied very systematically. Surface characterization, such as surface energy measurement, was carried out in order to investigate the effect of the wettability on the LC alignment properties of the polymer film. The synthesis and characterization of these polymer series and the optical properties of the fabricated LC cells made from polymer films were included.

Synthesis of Phenylphenoxymethyl-Substituted Polystyrene
PPHE#, phenylphenoxymethyl-substituted polystyrenes-where # is the molar fraction of the phenylphenoxymethyl side groups in the polymers-were synthesized by the procedure described below. As an example, the synthesis of the phenylphenoxymethyl-substituted polystyrene PPHE100 is presented. Poly(4-chloromethylstyrene) (PCMS, 1.97 milliequivalents of repeating units, 0.30 g) and 4-phenylphenol (150 mol % compared with PCMS, 2.95 mmol, 0.50 g) were dissolved in the N,N -dimethylacetamide (DMAc, 50 mL). Potassium carbonate (3.54 mmol, 0.611 g) was added to the 4-phenylphenol and PCMS mixture and then magnetically stirred at 70 • C for 24 h in a nitrogen atmosphere. In order to obtain a precipitate, the synthesized mixture in solution was poured into methanol after the mixture in solution was cooled at room temperature. The precipitate was filtered out and washed using a Soxhlet extractor with hot methanol in order to eliminate potassium carbonate and any residue. The PPHE100 obtained yields above 80% after drying overnight under vacuum. The degree (%) of substitution from PCMS to PPHE100 was interpreted by proton nuclear magnetic resonance ( 1 H NMR). Other polystyrene derivatives containing phenylphenoxymethyl side groups were synthesized by an analogous procedure used to prepare PPHE100 except for changing amounts of 4-phenylphenol in the reaction. For example, PPHE75, PPHE50, PPHE25, PPHE15, and PPHE5 were prepared with 4-phenylphenol of 0.25 g (1.48 mmol), 0.17 g (0.98 mmol), 0.083 g (0.49 mmol), 0.051 g (0.29 mmol), and 0.017 g (0.10 mmol), respectively, with slightly larger amounts of potassium carbonate (120 mol % compared with 4-phenylphenol). 1 H NMR assignments of the respective peaks of the polystyrene derivatives (PPHE75, PPHE50, PPHE25, PPHE15, and PPHE5) are as follows:

Film Preparation and LC Cell Assembly
Each solution of the PPHE# in tetrahydrofuran (1 wt %) was filtered by a poly(tetrafluoroet hylene) (PTFE) membrane that has a pore size of 0.45 µm. Thin polymer films were made through spin-coating (2000 rpm and 60 s) onto 2.0 × 2.5 cm 2 glass substrates using about 3.5 mL of 1 wt % THF solution of PPHE5, PPHE15, PPHE25, PPHE50, PPHE75, and PPHE100. The LC cells were made by assembling the prepared films using spacers that have a thickness of 4.25 µm. We selected 4 -pentyl-4-biphenylcarbonitrile (5CB) in fabricated LC cells to analyze the correlation between the alignment layer and LC molecules by physicochemical interaction because of the physicochemical properties of 5CB-such as its accessible nematic range near room temperature, good chemical stability, and high positive dielectric anisotropy, as reported in previous studies [63][64][65][66]. The fabricated cells were filled with nematic LCs (5CB) and were then sealed using epoxy glue.

Instrumentation
The proton nuclear magnetic resonance ( 1 H NMR) measurements were collected on Agilent MR400 DD2 (Agilent Technologies, Inc., Santa Clara, CA, USA) NMR spectrometer at a sample concentration of 20 mM deuterated solution. The average molecular weight (M n ) and polydispersity index (M w /M n ) of the synthesized polymer was measured by Waters gel permeation chromatography (GPC) with respect to monodisperse polystyrene standards using tetrahydrofuran as the eluent and a differential refractometer as the detector. A Q-10 (TA Instruments, Inc., New Castle, DE, USA) equipped with RCS40 (TA Instruments, Inc., New Castle, DE, USA) was employed to analyze thermal properties of the polymer by differential scanning calorimetry (DSC) at a heating rate of 10 • C/min and a cooling rate of 100 • C/min under a nitrogen atmosphere. The glass transition temperature (T g ) was detected in the second heating run over the range −40 to 200 • C. The contact angles were measured right away using a Krüss DSA10 (KRÜSS Scientific Instruments Inc., Hamburg, Germany) contact angle analyzer fitted with drop shape analysis software after deposing the water and diiodomethane droplets on the polymer films. The average volume of the droplets used for the contact angle measurement was 5 µL. The contact angles for each sample were determined four or more times on three independently prepared polymer films. The representative values were averaged. A Nikon Eclipse E600 POL (NIKON, Inc., Tokyo, Japan) fitted with a polarizer and Nikon, Coolpix 995 digital camera (NIKON Inc., Tokyo, Japan) was applied to take polarized optical microscopy (POM) images for the LC cell. In order to confirm the reliability to apply harsh environment, the ultraviolet (UV) stability of the LC cells was confirmed using a VL-6.LC lamp (λ max = 365 nm, Vilber Lourmat, Paris, France). A UV detector, GT-513 (Giltron, Seoul, Korea) was used to measure the intensity of irradiated UV light on the LC cells during UV light irradiation. The multi hotplate stirrer (DAIHAN Scientific Co., Ltd., Wonju, Korea) was used as a heating element to investigate the thermal stability of the LC cells. The LC cells were heated from room temperature to 100, 150, and 200 • C. The surface energy values were calculated by Owens-Wendt equation where, γ l is the surface energy of the liquid, γ sl is the interfacial energy of the solid/liquid interface, γ s is the surface energy of the solid, γ l d and γ l p are known for the test liquids, and γ s d and γ s p can be calculated from the measured static contact angles [67]. Figure 1 shows the route of synthesis for the phenylphenoxymethyl-substituted polystyrene, PPHE# (homopolymer PPHE100 and copolymers PPHE75, PPHE50, PPHE25, PPHE15, and PPHE5), where # is the molar content (%) of phenylphenoxymethyl side groups. As previously reported, the degrees of substitution reaction of the chlorine in poly(chloromethylstyrene) (PCMS) by nucleophilic compounds including the phenolate compounds, were observed to almost agree with feeding amount of the substitution [68,69]. The acidity of phenolic compounds was affected by the electron-withdrawing substituents group to the hydroxyl group [70,71]. The phenol group in the 4-phenylphenol can be easily dissociated to the phenolate and the proton, which is a strong nucleophile, since the structure of the phenolate anion could be stabilized by resonance structures. Furthermore, the benzylic carbon in the PCMS is relatively electron-deficient, due to the electron-withdrawing groups, viz. the chlorine and phenyl groups, which are attached directly to the carbon [72]. In addition, the structure of the transition state in the substitution reaction could be stabilized by conjugation with the benzene ring. Hence, the high conversion rate in the polymer modification reaction could be demonstrated by the electrophilicity of benzylic carbon in PCMS and the chemical structure stability of the phenolate anion as a nucleophile. The copolymers-PPHE5, PPHE15, PPHE25, PPHE50, and PPHE75-with different degree-of-substitution ratios (%) were obtained by varying the 4-phenylphenol amounts in the reaction. Conversions from chloromethyl to phenylphenoxymethyl group are almost 100% when 150 mol % of phenylphenoxymethyl was used at 70 • C for 24 h, as determined in the assignment of the corresponding proton peaks of the phenylphenoxymethyl-substituted polystyrene PPHE100. The mole percent of phenylphenoxymethyl containing monomeric units in the obtained polymers was demonstrated by proton nuclear magnetic resonance ( 1 H NMR) measurement. The 1 H NMR spectra and assignments of the respective peaks of the polymers-such as PPHE100, PPHE75, PPHE50, PPHE25, PPHE15, and PPHE5-can be seen from Figure 2. The 1 H NMR spectrum of PPHE100 (Figure 2f) is explained as an example. The 1 H NMR spectrum of PPHE100 indicated the presence of protons of the phenyl ring in the styrene backbone and the proton peaks from the phenyl ring in the phenylphenoxymethyl side chains (δ = 6.3-7.7 ppm (peak a)). In addition, the proton peaks from alkyl groups of oxymethyl and styrene backbone were identified at (δ = 4.6-5.2 ppm (peak b) and δ = 1.1-2.0 ppm (peak c)). The degree of substitution from chloromethyl to phenylphenoxymethyl was calculated to be almost 100% by comparing the integral ratio of the phenylphenoxymethyl peaks at 6.3-7.7 ppm and the backbone peaks at 1.1-2.0 ppm. Similar integrations and calculations for PPHE5, PPHE15, PPHE25, PPHE50, and PPHE75 were performed, and results were generally within ±10% of the expected values of synthesis. These prepared polymers showed good solubility in medium-polarity solvents that have low boiling points, including THF and chloroform. All samples exhibited a good solubility in various solvents for the application of PPHE# as thin-film materials. We selected THF as the coating solvent to make thin-film materials, because of its low toxicity and good biodegradability [73]. These polymer films can be fabricated using a wet process at a low temperature for next-generation applications.

Results and Discussion
Polymers 2022, 14, x FOR PEER REVIEW 6 of 14 the proton peaks from the phenyl ring in the phenylphenoxymethyl side chains (δ = 6.3-7.7 ppm (peak a)). In addition, the proton peaks from alkyl groups of oxymethyl and styrene backbone were identified at (δ = 4.6-5.2 ppm (peak b) and δ = 1.1-2.0 ppm (peak c)). The degree of substitution from chloromethyl to phenylphenoxymethyl was calculated to be almost 100% by comparing the integral ratio of the phenylphenoxymethyl peaks at 6.3-7.7 ppm and the backbone peaks at 1.1-2.0 ppm. Similar integrations and calculations for PPHE5, PPHE15, PPHE25, PPHE50, and PPHE75 were performed, and results were generally within ±10% of the expected values of synthesis. These prepared polymers showed good solubility in medium-polarity solvents that have low boiling points, including THF and chloroform. All samples exhibited a good solubility in various solvents for the application of PPHE# as thin-film materials. We selected THF as the coating solvent to make thin-film materials, because of its low toxicity and good biodegradability [73]. These polymer films can be fabricated using a wet process at a low temperature for next-generation applications.   the proton peaks from the phenyl ring in the phenylphenoxymethyl side chains (δ = 6.3-7.7 ppm (peak a)). In addition, the proton peaks from alkyl groups of oxymethyl and styrene backbone were identified at (δ = 4.6-5.2 ppm (peak b) and δ = 1.1-2.0 ppm (peak c)). The degree of substitution from chloromethyl to phenylphenoxymethyl was calculated to be almost 100% by comparing the integral ratio of the phenylphenoxymethyl peaks at 6.3-7.7 ppm and the backbone peaks at 1.1-2.0 ppm. Similar integrations and calculations for PPHE5, PPHE15, PPHE25, PPHE50, and PPHE75 were performed, and results were generally within ±10% of the expected values of synthesis. These prepared polymers showed good solubility in medium-polarity solvents that have low boiling points, including THF and chloroform. All samples exhibited a good solubility in various solvents for the application of PPHE# as thin-film materials. We selected THF as the coating solvent to make thin-film materials, because of its low toxicity and good biodegradability [73]. These polymer films can be fabricated using a wet process at a low temperature for next-generation applications.   The thermal properties of these polymers, PPHE#, were studied using differential scanning calorimetry (DSC), and all polymers exhibited amorphous behavior, because only the glass transition was found from their DSC thermogram. The T g values of polystyrene derivatives slightly increased or decreased according to the different molar content of the side group as shown in Figure 3. As described in the previous studies, the T g of the polymers was affected by two main factors-chain flexibility and intermolecular interaction [74]. The changes in T g of polymer were determined by interplay between these two effects. For example, the decrease in T g values of the PS derivatives with increasing molar content of the bulky phenylphenoxymethyl side chains in the polymer was ascribed to the increase in steric volume in the polymer, as previously reported [75][76][77], while the increase in the T g values of the PS derivative was attributed to an increase in the π-π and van der Waals interactions among the phenylphenoxymethyl side chains [75,76,78,79]. The T g values of PPHE5, PPHE15, PPHE25, PPHE50, PPHE75, and PPHE100 are 108.1, 109.6, 106.9, 104.9, 105.0, and 106.7 • C. In conclusion, the T g value of the PS derivatives is determined by a play-off between the free volume effect and the intermolecular interaction effect of the polymer chain. It was found that the T g values of these polymers, PPHE#s, were higher than 100 • C due to their aromatic structure in the biphenyl-based PHE moiety. This result suggests that polystyrene substituted with phenylphenoxymethyl (PPHE#) containing the aromatic biphenyl moiety-a representative precursor in LC molecules-has a thermal stability which is higher than that of the previously reported PS derivatives containing alkyl aromatic LC precursors in the polymer-such as 4-(trans-4-ethylcyclohexyl)phenol [58], ethyl-p-hydroxybenzoate [59], and 4-ethyloxyphenol [60].
The thermal properties of these polymers, PPHE#, were studied using differential scanning calorimetry (DSC), and all polymers exhibited amorphous behavior, because only the glass transition was found from their DSC thermogram. The Tg values of polystyrene derivatives slightly increased or decreased according to the different molar content of the side group as shown in Figure 3. As described in the previous studies, the Tg of the polymers was affected by two main factors-chain flexibility and intermolecular interaction [74]. The changes in Tg of polymer were determined by interplay between these two effects. For example, the decrease in Tg values of the PS derivatives with increasing molar content of the bulky phenylphenoxymethyl side chains in the polymer was ascribed to the increase in steric volume in the polymer, as previously reported [75][76][77], while the increase in the Tg values of the PS derivative was attributed to an increase in the π-π and van der Waals interactions among the phenylphenoxymethyl side chains [75,76,78,79].
The Tg values of PPHE5, PPHE15, PPHE25, PPHE50, PPHE75, and PPHE100 are 108.1, 109.6, 106.9, 104.9, 105.0, and 106.7 °C. In conclusion, the Tg value of the PS derivatives is determined by a play-off between the free volume effect and the intermolecular interaction effect of the polymer chain. It was found that the Tg values of these polymers, PPHE#s, were higher than 100 °C due to their aromatic structure in the biphenyl-based PHE moiety. This result suggests that polystyrene substituted with phenylphenoxymethyl (PPHE#) containing the aromatic biphenyl moiety-a representative precursor in LC molecules-has a thermal stability which is higher than that of the previously reported PS derivatives containing alkyl aromatic LC precursors in the polymer-such as 4-(trans-4ethylcyclohexyl)phenol [58], ethyl-p-hydroxybenzoate [59], and 4-ethyloxyphenol [60]. It is widely known that the LC alignment behavior can be affected by the interactions at the interface between alignment layer and LC molecules [80][81][82]. Therefore, LC cells made using films of phenylphenoxymethyl-substituted polystyrene derivatives structurally similar to LC molecules were fabricated using 5CB to study the LC alignment behavior of the polymer films. The LC cells fabricated from PPHP# films with a phenylphenoxymethyl side group content of less than 15 mol % (PPHP5 and PPHP15) showed planar LC alignment behavior, while good uniformity of vertical LC alignment behavior was observed for LC cells fabricated with the polymer films with a phenylphenoxymethyl side group content of at least 25 mol % (PPHP25, PPHP50, PPHP75, and PPHP100). We investigated the LC alignment performance on PPHE# films by observing their polarized optical microscopy (POM) images, as can be seen from Figure 4. A random planar LC alignment performance was observed for the LC cells made using the PCMS film (figure not shown). As the molar content of the phenylphenoxymethyl containing a monomeric unit in the PPHE# was 5 and 15 mol %, the LC cells fabricated with the PPHE# film exhibited It is widely known that the LC alignment behavior can be affected by the interactions at the interface between alignment layer and LC molecules [80][81][82]. Therefore, LC cells made using films of phenylphenoxymethyl-substituted polystyrene derivatives structurally similar to LC molecules were fabricated using 5CB to study the LC alignment behavior of the polymer films. The LC cells fabricated from PPHP# films with a phenylphenoxymethyl side group content of less than 15 mol % (PPHP5 and PPHP15) showed planar LC alignment behavior, while good uniformity of vertical LC alignment behavior was observed for LC cells fabricated with the polymer films with a phenylphenoxymethyl side group content of at least 25 mol % (PPHP25, PPHP50, PPHP75, and PPHP100). We investigated the LC alignment performance on PPHE# films by observing their polarized optical microscopy (POM) images, as can be seen from Figure 4. A random planar LC alignment performance was observed for the LC cells made using the PCMS film (figure not shown). As the molar content of the phenylphenoxymethyl containing a monomeric unit in the PPHE# was 5 and 15 mol %, the LC cells fabricated with the PPHE# film exhibited random planar LC alignment in the conoscopic POM images. In contrast, at a molar content of 25-100 mol %, the LC cells fabricated with the PPHE# film exhibited a uniform vertical LC alignment, and it can be confirmed by the Maltese cross pattern of the conoscopic POM images. Based on the LC alignment results, we observed a general tendency that the polymers having higher random planar LC alignment in the conoscopic POM images. In contrast, at a molar content of 25-100 mol %, the LC cells fabricated with the PPHE# film exhibited a uniform vertical LC alignment, and it can be confirmed by the Maltese cross pattern of the conoscopic POM images. Based on the LC alignment results, we observed a general tendency that the polymers having higher molar content of phenylphenoxymethyl side groups with a similar molecular structure prefer vertical LC alignment. It is widely known that the vertical alignment behavior of the LC molecules on the alignment layer could be ascribed to the surface energy of the alignment layer which is smaller than the surface tension of the LC [83][84][85][86]. Therefore, we demonstrated the LC alignment behaviors of the PPHE# films using surface energy measurements, one of the surface characterization techniques. Figure 5 and Table 1  increasing the molar content of the phenylphenoxymethyl moiety in the side groups. We found that the vertical LC alignment performance correlates well with the polar surface energy of the PPHE# films. As shown in several studies, the polar surface energy of the alignment layer can affect the LC alignment performances [86][87][88]. Therefore, it is suggested that the vertical LC alignment behavior is affected by the polar surface energy of the polymer films which is lesser than approximately 4.2 mJ/m 2 due to the unique structure of the phenylphenoxymethyl side chain.  It is widely known that the vertical alignment behavior of the LC molecules on the alignment layer could be ascribed to the surface energy of the alignment layer which is smaller than the surface tension of the LC [83][84][85][86]. Therefore, we demonstrated the LC alignment behaviors of the PPHE# films using surface energy measurements, one of the surface characterization techniques. Figure 5 and Table 1  increasing the molar content of the phenylphenoxymethyl moiety in the side groups. We found that the vertical LC alignment performance correlates well with the polar surface energy of the PPHE# films. As shown in several studies, the polar surface energy of the alignment layer can affect the LC alignment performances [86][87][88]. Therefore, it is suggested that the vertical LC alignment behavior is affected by the polar surface energy of the polymer films which is lesser than approximately 4.2 mJ/m 2 due to the unique structure of the phenylphenoxymethyl side chain. In order to confirm the reliability of LC cells composed of the polymer films, a stability test of the LC alignment performance was carried out under the harsh conditions, viz. high temperature and ultraviolet (UV) exposure. The thermal and UV stabilities of the LC cells made from the PPHE100 films were demonstrated from the POM image after heating and ultraviolet irradiation (Figure 6). In the case of the thermal stability test, the LC cells fabricated with PPHE100 films were heated using the hot plate for 10 min under different  In order to confirm the reliability of LC cells composed of the polymer films, a stability test of the LC alignment performance was carried out under the harsh conditions, viz. high temperature and ultraviolet (UV) exposure. The thermal and UV stabilities of the LC cells made from the PPHE100 films were demonstrated from the POM image after heating and ultraviolet irradiation ( Figure 6). In the case of the thermal stability test, the LC cells fabricated with PPHE100 films were heated using the hot plate for 10 min under different temperatures at room temperature, 100, 150, and 200 • C, respectively. Furthermore, in order to confirm the UV stability of LC cells fabricated with PPHE100 films, the LC cells were irradiated with UV rays at 5, 15, and 20 J/cm 2 , respectively. As shown in Figure 6, no distinguishable difference in the vertical LC alignment of the LC cells prepared from PPHE100 films could be observed from the conoscopic POM images, indicating that the vertical LC aligning ability was maintained when heated at 200 • C for 10 min and irradiated with exposure energy of 20 J/cm 2 . Therefore, PPHE100 LC cell can be applied to high temperature and UV irradiation conditions. It is important to align the anisotropic materials in one direction, such as the liquid crystal elastomers (LCEs) and photocurable materials in LC composite system, as well as cyanobiphenyl-based LC which is one of the small molecule LCs. We believe that comb-like polystyrene derivatives having low processing temperature and good optical transparency and high solubility in common organic solvent can be a suitable candidate of the alignment layer for future applications in biomedical, LC laser, and 4D printing using LCs [89][90][91][92].

Conclusions
A copolymer series of polystyrene substituted with phenylphenoxymethyl (PPHE#) containing the biphenyl moiety, a representative precursor in LC molecules, was synthesized in order to evaluate the LC alignment behavior of the polymer films. Interestingly, the LC cells made from the films of phenylphenoxymethyl-substituted polystyrene having only an additional phenylphenoxymethyl side group showed vertical LC alignment behavior. The vertical LC aligning ability was observed for the LC cells made using the polymer films with a higher molar content of phenylphenoxymethyl side groups. The LC cells made from polymer films having 25 mol % or more of phenylphenoxymethyl (PPHE25, PPHE50, PPHE75, and PPHE100) side groups showed vertical LC aligning abil-

Conclusions
A copolymer series of polystyrene substituted with phenylphenoxymethyl (PPHE#) containing the biphenyl moiety, a representative precursor in LC molecules, was synthesized in order to evaluate the LC alignment behavior of the polymer films. Interestingly, the LC cells made from the films of phenylphenoxymethyl-substituted polystyrene having only an additional phenylphenoxymethyl side group showed vertical LC alignment behavior. The vertical LC aligning ability was observed for the LC cells made using the polymer films with a higher molar content of phenylphenoxymethyl side groups. The LC cells made from polymer films having 25 mol % or more of phenylphenoxymethyl (PPHE25, PPHE50, PPHE75, and PPHE100) side groups showed vertical LC aligning ability, while the LC cells-made from PPHE# films having less than 25 mol % of phenylphenoxymethyl side groups-exhibited random planar LC alignment. These results suggest that the LC precursor structures in the polymer side chains can be advantageous in the vertical alignment of LC molecules. The vertical LC alignment behavior was correlated with polymer films that have polar surface energies lower than 4.2 mJ/m 2 , due to the unique structure of the phenylphenoxymethyl side chain. Therefore, phenylphenoxymethyl-substituted polystyrenes could be promising candidates for the LC alignment layer for next-generation applications using wet processes at low temperatures. This work can provide the basic information for the design of the LC alignment layer using LC precursors containing polymer films.

Institutional Review Board Statement: Not applicable.
Informed Consent Statement: Not applicable.

Data Availability Statement:
The data presented in this study are available on request from the corresponding author.
Acknowledgments: Financial support from the Dong-A University Research Fund is gratefully acknowledged.

Conflicts of Interest:
There are no conflicts to declare.