Amplifying Chiroptical Properties of Conjugated Polymer Thin-Film Using an Achiral Additive.

Chiral conjugated polymers bearing enantiopure side chains offer the possibility to harness the effect of chirality in organic electronic devices. However, its use is hampered by the low degree of circular polarization in absorption (gabs) in most of the conjugated polymer thin-films studied. Here we demonstrate a versatile method to significantly increase the gabs by using a few weight percentages of a commercially available achiral long-chain alcohol as an additive. This additive enhances the chiroptical properties in both absorption and emission by ca. 5-10 times in the thin-films. We envisage that the alcohol additive acts as a plasticizer which enhances the long-range chiral liquid crystalline ordering of the polymer chains, thereby amplifying the chiroptical properties in the thin-film. The application of this methodology to various conjugated polymers has been demonstrated.

Introduction

Conjugated semiconducting polymers form the active component of organic electronic devices such as solar cells, light-emitting diodes, and field-effect transistors.[1−3] Most of the conjugated polymers studied bear achiral or branched, but racemic, side chains to provide better solubility in common organic solvents used for processing.[4] On the other hand, conjugated polymers bearing enantiopure chiral side chains display new functionalities.[5,6] Circularly polarized photo- and electroluminescent devices based on chiral conjugated oligomers and polymers have been studied for application in advanced display technology.[7−10] Furthermore, chirality of the molecular semiconductor has been utilized to construct chiral sensors[11] and to detect circularly polarized light.[12] The enantiopure molecular materials can show chiral-induced spin-selectivity,[13] and thus chiral molecular semiconductors can be applied as spin-filters.[14] The impact of the chirality of a semiconductor was further demonstrated by Fuchter and co-workers, where they observed over 80-fold difference in the hole mobility of 1-aza[6]-helicene in the thin-film state between enantiopure and racemic mixture.[15] Thus, it is clear that chirality of a system or chiral supramolecular organization attained through enantiomerically pure side chains can directly impact the desired functionality.[5,6] In order to exploit the manifestation of chirality in semiconductor devices, it is paramount to achieve and control high degree of circular polarization (defined as g = 2 × [(IL – IR)/(IL + IR)], where IL and IR are the intensities of left and right circularly polarized light absorbed (gabs) or emitted (gPL), respectively) of chiral conjugated polymer thin-films.

Various approaches to achieve high g-values (gabs, gPL, and gEL) in molecular systems can be broadly classified into two main categories, namely, based (i) on molecular or local origin, and (ii) on long-range ordering or a nonlocal mechanism. The local origin of photo- and electroluminescence (gEL > 1) is observed for lanthanide[16−18] and platinium[19] complexes with chiral ligands. Since the emission originates at a molecular level, the observed g-values are independent of the long-range ordering in the system. Although this approach yields high g-values, it has a few shortcomings, namely, a low photoluminescence quantum yield, an electronically forbidden transitions in metal complexes leading to narrow emission band, and finally the structurally unique chiral ligands such as helicenes further limiting the scope of this approach.

On the other hand, Chen and co-workers have shown that chiral oligo(fluorenes)[8,20] exhibit highly ordered chiral liquid crystalline phases such as cholesterics in annealed films with g-values >0.1. The cholesteric ordering has been mainly observed for poly(fluorene) homopolymers,[21,22] copolymer,[23−26] and poly(p-phenyleneethynylene)s[27] which exhibited g-values ranging from 0.1 to 1 in annealed thin-films. Unlike the metal complexes discussed previously, the chiral poly(fluorene)s[28,23] and poly(thiophene)s[29] show a strong film-thickness dependence of gabs, indicating that the long-range cholesteric ordering dictates the g-value in such systems. Chiral poly(fluorene-alt-benzothiadiazole) (c-PFBT) has been shown to form a multidomain cholesteric organization with high g-values,[23,30] and this has been utilized to achieve highly circularly polarized OLEDs.[9] To enhance the chiral organization of c-PFBT through cholesteric ordering and plasmonic effect, Prasad and co-workers have used gold nanoparticles (diameter 4–10 nm) as additive to c-PFBT polymer, and annealing the nanocomposite films resulted in enhanced circular dichroism effect.[31] Further, an alternative route to induce cholesteric organization and high g-values to conjugated polymers was successfully demonstrated by the addition of a chiral dopant with high helical twisting power to an achiral conjugated polymer such as poly(9,9′-dioctylfluorene-alt-benzothiadiazole) (F8BT).[32,33] In spite of the above-mentioned efforts, a vast number of enantiopure chiral conjugated polymers exhibit no apparent cholesteric organization, thus impeding their applications.

Here we have developed a generally applicable and facile method to significantly enhance the chiroptical properties of conjugated polymer thin-films. Our approach uses a cheap, commercially available, and achiral additive to improve the chiral liquid crystalline ordering of enantiopure conjugated polymer thin-films, thus leading to significantly enhanced chiroptical properties. To study the effect of the additive, we have chosen the chiral analogues of a known archetypical red-emitting diketopyrrolopyrrole (DPP) alternating fluorene copolymer.[34] First, we show the effect of the additive on the chiroptical and photophysical properties of the polymer. Then, we shed light on the influence of the additive on the mesoscopic organization of the polymer, and finally we conclude by showing the general applicability of the approach to other conjugated polymers.

Results and Discussion

All the three fluorene-alt-DPP polymers (Figure a) were synthesized by Suzuki-polycondensation and characterized using 1H-, 13C NMR, and GPC (See Supporting Information Figures S1–S18). All polymers showed good thermal stability without any degradation until 300 °C (Figure S19). Further thermal analysis by differential scanning calorimetry (DSC) showed that all polymers exhibit only a weak endothermic transition at high temperatures, without any discernible glass-transition temperature (Figure S20). Polarized optical microscopy (POM) images of F8*- polymer recorded under cross-polarizer showed that around the weak endothermic transition observed in DSC, the polymer becomes more fluidic, and the birefringence increases and moreover the birefringence is retained on further cooling the sample to room temperature (Figure S21). Thus, based on DSC and POM results, we designate the temperature at which polymer transitions from a less ordered amorphous to ordered, birefringent phase as Ttrans. Due to the rather weak and broad Ttrans transition, all the polymers thin-films were annealed at higher temperature (280 °C) to ensure the complete transition. The thermal and molecular weight distribution of the polymers are presented in Table S1. Most of the studies here will be focused on F8*- polymer, where the asterisk sign indicates the position of the chiral unit.

Figure 1

Enhancing chiroptical properties with an additive. (a) Structure of the fluorene copolymers investigated in this study. Asterisk sign indicates the position of the chiral side chains. (b) Structure and important physical properties of the achiral polyethylene monoalcohol (PEM-OH) used as a processing additive. (c) CD spectra of F8*- films embedded with different weight percentage of PEM-OH at 20 °C. The films were annealed at 280 °C for 15 min and cooled down to room temperature before measuring CD spectra. Arrow indicates spectral changes with increasing weight percentage of PEM-OH. (d) |gabs| at CD maximum as a function of weight percentage of PEM-OH based on CD spectra shown in (c). The solid black line is a guide to the eye to indicate the trend in |gabs|. The gray bar indicates the percentage around which maximum enhancement is observed. Typical film thickness = 120 ± 20 nm.

Enhancing Chiroptical Properties of F8*- Thin-Films with an Additive

The pristine films (∼120 ± 20 nm) of F8*- spin-coated from a chloroform solution on glass substrate did not exhibit any Cotton effect (Figure S22a). Upon annealing, a clear Cotton effect was observed, and the maximum effect was seen when annealed at 280 °C (Figure S22a), beyond the Ttrans of the polymer (∼240 °C). The gabs was found to be −5 × 10–3 (at 540 nm), which is in similar range as observed for most of the conjugated polymers in thin-films. The low magnitude of the gabs can be explained by the local chiral ordering of the polymer chains.

In order to enhance the chiroptical properties of F8*- in the thin-film, here we have chosen the commercially available alcohol, namely, polyethylene monoalcohol (PEM-OH) with an average 48 methylene units and a Tm of 108–110 °C as an additive (Figure b). First we look at the effect of the additive on the Cotton effect at a constant film thickness (∼120 ± 20 nm). The PEM-OH and F8*- were mixed in a good solvent and spin-coated on glass substrates and annealed beyond the Ttrans and Tm of both F8*- and PEM-OH, respectively, and finally the CD spectra of thin-films were recorded at 20 °C (see the Methods section for detailed procedure). The CD spectra show a pronounced enhancement in Cotton effect with addition of small amount (2–6 wt %) of PEM-OH. The sign of the Cotton effect is unaffected, and only the magnitude increases with addition of PEM-OH. The enhancement in magnitude of the Cotton effect saturates around 6–8 wt %, and with further increase in the amount of PEM-OH, a small decrease in the magnitude of the Cotton effect was observed (Figure c). We noticed a 15–20 nm red-shift of the CD maximum going from 0 to 40 wt % of PEM-OH. To quantify the enhancement in chiroptical properties, we study the evolution of gabs with addition of PEM-OH. The gabs changes from −5 × 10–3 for pristine polymer film to −6 × 10–2 for 8 wt % of PEM-OH blended films (Figure d). The gabs remained −5 ± 1 × 10–2 with addition of higher weight percentage of PEM-OH. Linear dichroism spectra on films with different weight percentage of PEM-OH showed negligible anisotropy in the films (Figure S23), indicating that such artifacts do not contribute significantly to the observed CD signals. For all the different weight percentages of PEM-OH, the UV–vis absorption spectra of the polymer remain unaltered in the thin-film (Figure S24). Similarly, both the steady-state and time-resolved photoluminescence spectra of F8*- are unaltered by the addition of PEM-OH (Figure S25), suggesting no electronic perturbation of the F8*- on addition of PEM-OH.

As it has been previously shown that gabs strongly depends on the film thickness for fluorene-based polymers,[28] we have looked into the film-thickness dependence of gabs for F8*- both without and with PEM-OH. Annealed thin-films of F8*- (without PEM-OH) show an increase in gabs from −0.002 (80 nm) to −0.034 (200 ± 10 nm) with an increase in film thickness (Figure a). Further, by combining the effect of PEM-OH (8 wt %) with the film-thickness dependence we could observe significant enhancement in gabs, and a maximum gabs of −0.13 could be achieved for a film thickness of 240 ± 20 nm (Figure a). This indicates that both the effect of PEM-OH and film-thickness dependence operate synergistically to achieve high |gabs| (>0.1) in annealed films.

Figure 2

(a) Thickness dependence of |gabs| for F8*- annealed thin-films without and with (8 wt %) PEM-OH. The solid lines is a guide to the eye to indicate the trend. Error bars in the film thickness indicate the thickness distribution on different parts of the film. (b) Degree of circular polarization in photoluminescence (gPL) without and with (8 wt %) of PEM-OH when excited at 356 nm. The weight percentage of the PEM-OH and film thickness are mentioned in (b). All the films were annealed at 280 °C for 15 min, and the spectra are recorded at 20 °C.

We have further investigated the influence of the PEM-OH additive and film thickness on the degree of circular polarization in photoluminescence (gPL) for F8*-. Pristine annealed F8*- film (thickness of 120 nm) shows a gPL of −0.0019 (at 573 nm). For a film of similar thickness with 8 wt % of PEM-OH, a gPL of −0.048 (at 583 nm) was observed, showing >25 times increase in gPL on addition of PEM-OH. Combining both the effects of adding PEM-OH (8 wt %) and film thickness (240 ± 20 nm), gPL of −0.11 (at 583 nm) was observed with an enhancement in gPL of >50 times compared to the pristine annealed films of F8*-. Thus, the PEM-OH additive can lead to significant enhancement in chiroptical properties (gabs and gPL).

To understand the origin of the enhancement on addition of PEM-OH, we first studied if the alcohol group of PEM-OH is really necessary for amplification of chiroptical properties in the thin-film. In place of PEM-OH, a linear chain alkane with 42 methylene units (C44H90, tetratetracontane), similar to the number of methylene units in PEM-OH, was used as an additive. The CD spectra of the pristine annealed film and with 7 wt % of tetratetracontane were identical (Figure S26a), indicating no enhancement in gabs on addition of tetratetracontane. It is to be noted that with PEM-OH at similar weight percentage (6–8 wt %), the maximum enhancement was already observed. However, with 20 wt % of tetratetracontane the gabs increased to −0.02, an enhancement of <2 times compared to the pristine films (Figure S26c). This suggests that alcohol group on the long-chain alkane is important in achieving high enhancement factor. Further, we have also looked into the role of polymer self-assembly in alcohol as solvent and its relation to the enhancement in chiroptical properties in thin-film. First we studied F8*-, which showed significantly high gabs (∼ −0.02) when self-assembled in dilute n-butanol as solvent (Figure S27), and it was also observed that addition of PEM-OH resulted in improved gabs in annealed thin-film (Figure c). However, F8-, a structural isomer of F8*- with chiral side chains on the DPP unit, did not show any Cotton effect (helical organization) in n-decanol (Figure S28a), and also the annealed thin-films of F8- with PEM-OH additive showed low gabs of 10–3 (Figure S28b, c). Where the solution experiments give evidence for the presence of a chiral packing in nanosized aggregates, the thin-film experiments show the presence of macroscopic chiral liquid crystalline ordering. Apparently, the need for a nanoscopic local arrangement is amplified macroscopically.

Morphological Characterization of Pristine and PEM-OH Blended Films

Having established the importance of polymer self-assembly in alcohols as solvent and the role of alcohol group of PEM-OH in enhancement of chiroptical properties, we further investigated the interaction of PEM-OH with F8*- polymer chains. The FT-IR spectra of F8*- thin-films (∼120 nm) without and with 5–20 wt % of PEM-OH showed no clear shifts in both the C=O stretching of the DPP units and the C–H stretching of the alkyl chains (Figure S29), suggesting no chemical interactions between F8*- and PEM-OH. The effect of the PEM-OH on mesoscopic organization of F8*- was further investigated by polarized optical microscopy (POM). POM images of pristine annealed films (∼165 ± 10 nm) show birefringence without a clear texture. However, on closer examination we see small features (3–6 μm) reminiscent of nematic ordering (Figure a). On the other hand, the 10 wt % PEM-OH blended films shows clear birefringence with large domains (10–20 μm) present through most part of the film (Figure b). This suggests that, on addition of PEM-OH, the chiral liquid crystalline ordering in the sample gets enhanced. The effect of PEM-OH on surface topography was studied through tapping-mode atomic force microscopy (AFM). The AFM height images of pristine annealed F8*- films shows a network of fibers with a very smooth surface (±14 nm, Figure c). However, the 10 wt % blended films show platelet like topography with an increased surface roughness of 80–100 nm (Figure d). The lack of fibrillary morphology indicates marked difference between the pristine and PEM-OH blended films. Further differential scanning calorimetric (DSC) studies were carried out to study the bulk phase behavior of polymer on addition of PEM-OH. Pristine polymer shows weak transition (Ttrans) around 230–240 °C (Figure S30). With 12.5 wt % of PEM-OH embedded into the polymers, first the melting of PEM-OH was observed at 108–112 °C, and with further heating near the Ttrans of F8*- a clear exothermic transition was observed (Figure S30). This exothermic peak (cold crystallization) on the heating run indicates ordering of polymer and PEM-OH mixture near the Ttrans of F8*-.

Figure 3

Morphological characterization of the effect of PEM-OH on F8*- annealed thin-films. (a) and (b) Polarized optical microscopy image of F8*- annealed films without and with 10 wt % of PEM-OH, respectively, under crossed polarizers. The white circles indicate regions in which a nematic like texture is observed. Note that the size of regions is much larger in (b) compared to (a). The thickness of film for POM images was 165 ± 10 nm. (c) and (d) Tapping mode atomic force microscopy height images of F8*- annealed films without and with 10 wt % PEM-OH, respectively. Note that the scale bar for both (c) and (d) is the same (1 μm). The film thickness for AFM studies was ∼120 nm.

In order to study this ordering, bulk wide-angle X-ray scattering (WAXS) experiments were performed. The WAXS profile of annealed F8*- shows a principal peak at 0.35 Å–1 corresponding to a distance of 17.5 Å which matches well with the distance between the fully elongated chiral chains on the fluorene (Figure S31a, b). In addition to the principal peak, other weak peaks at 0.68 and 1.21 Å–1 and a broad halo centered at 1.38 Å–1 were observed. These features suggests that F8*- exhibits a semicrystalline organization, and this is also consistent with the disordered fibrillary morphology observed in AFM (Figure c). On addition of PEM-OH, only minor changes were observed in the WAXS profile, suggesting that the semicrystalline nature of F8*- is maintained (Figure S31c). It is worth noting that the liquid crystalline ordering observed in POM on addition of PEM-OH is at a much larger length scale (few micrometers) compared to local ordering (nanometer scale) probed using WAXS measurements.

Based on DSC, POM, and AFM studies, the structural evolution of the F8*- on addition of PEM-OH can be visualized as shown in Figure . At room temperature (either in thin-film or bulk), both PEM-OH and the semicrystalline F8*- exist as physical mixture (Figure a). On heating beyond the melting point of PEM-OH, it melts and blends into the matrix of F8*- (Figure b). On further heating near the Ttrans of the polymer, the polymer softens or in other words the semicrystalline regions in the polymer melt (Figure c), and it now interacts with the molten PEM-OH leading to cold crystallization or ordering into a nematic-like phase (Figure d). Thus, the PEM-OH enhances the chiroptical properties in the thin-film by improving the chiral liquid crystalline ordering of the polymer chains without a direct chemical interaction with the polymer chains.

Figure 4

Schematic illustration of the influence of PEM-OH on the morphology of the conjugated polymer. The glass substrate is depicted in gray, the black lines represent polymer chains, the yellow lines indicate PEM-OH, and the cyan regions illustrate the semiordered regions in the sample. (a) Shows the physical mixture of crystalline PEM-OH and semicrystalline polymer at room temperature. (b) Around the melting point of PEM-OH, the crystallites of PEM-OH break down, and the polymer does not undergo any changes. On furthering heating until Ttrans or Tm of polymer, both polymer and PEM-OH mix (c) and instantaneously undergo cold-crystallization (d) leading to ordered regions containing PEM-OH (the cyan regions in (d)).

Generality of the PEM-OH Methodology

Finally, we have looked into the general applicability of the PEM-OH methodology to enhance chiroptical properties in other π-conjugated polymers. The polymers we have chosen are the fully chiral F8*-, c-PFBT, and chiral poly(thiophene) (PBMBT) (Figure a and 5a). F8*- and c-PFBT polymers self-assemble in n-decanol with gabs of 0.008 and −0.07, respectively (Figure S32). Chiral poly(thiophene) (PBMBT) has also been observed to show significantly high gabs (∼0.08) in n-decanol as solvent at low concentration.[35,36] Further, the PEM-OH embedded films indeed show an enhancement of 10 and 5 times for F8*- and c-PFBT, respectively (see Figure S33, Figure S34, Figure b, and Table ). Annealed PBMBT films blended with different weight percentage of PEM-OH also showed improved chiroptical properties (Figure S35, Figure b), but the maximum gabs was observed around 30 wt % of the additive (Table ).

Figure 5

Application of PEM-OH addition strategy to other π-conjugated polymers. (a) Chemical structure of c-PFBT and PBMBT. (b) Evolution of |gabs| at the maximum of CD effect in annealed thin-films as a function of different weight percentage of PEM-OH. The black solid is a guide to the eye. c-PFBT, PBMBT, and F8*- films were annealed at 150, 170, and 280 °C, respectively, for 15 min and cooled down. Thicknesses of c-PFBT, PBMBT, and F8*- films were 90 ± 10, 80 ± 20, and 120 ± 10 nm, respectively. All the CD spectra were recorded at 20 °C.

Table 1

Comparison of Chiroptical Properties of Different Polymers with and without PEM-OH

polymer	gabs for pristine filmsa (gabs,prist)	max. gabs for PEM–OH blended filmsa (gabs, PEM-OH) (wt % of PEM-OH)b	enhancement factor (gabs,PEM–OH/gabs,prist)	gPL for pristine filmsa	max. gPL for PEM-OH blended filmsa
F8*-alt-DPP	–5 × 10–3	–6 × 10–2 (8 wt %)	12	–9 × 10–3	5 × 10–2
F8*-alt-DPP*	–8 × 10–2	–1 × 10–1 (10 wt %)	12.5	N.D.	N.D.
c-PFBT	–4 × 10–2	–2 × 10–1 (10 wt %)	5	–3 × 10–2	2.4 × 10–1
PBMBT	–1 × 10–3	–9 × 10–2 (30 wt %)	6–8	N.D.	N.D.

Annealed films.

The values in the parentheses indicate the percentage were maximum gabs was observed, N.D.: not determined.

Further the PBMBT films annealed at 120 °C (below the Tm ∼ 160 °C of polymer) did not show any enhancement in Cotton effect (Figure S36). However, when the films were annealed at 170 °C, that is, beyond the Tm of both the PEM-OH (108–110 °C) and PBMBT (∼160 °C), the gabs was significantly enhanced (Figure b and Figure S35). This indicates that annealing beyond the Tm of both PEM-OH and the polymer is necessary for them to undergo intermixing and leading to more ordered organization. DSC thermogram of PBMBT with 4 wt % of PEM-OH showed improved crystallization compared to the pristine polymer (Figure S37). Similarly, F8*- also showed a strong cold crystallization with 27 wt % of PEM-OH at ∼230 °C (Ttrans of the polymer, Figure S38). These observations are similar to that seen for F8*-, indicating that a similar mechanism of enhancement is operative for these polymers as well.

Furthermore, the PEM-OH blended films of c-PFBT show gPL reaching −0.2 to −0.3 at higher weight percentage of PEM-OH (Figure S39). It is noteworthy that c-PFBT was previously shown to exhibit high gabs (∼0.15) at an optimum of molecular weight.[23] However, in the present study we have utilized the as synthesized polydisperse sample without fractionation and could still achieve higher gabs (>0.2) than those observed for the optimum molecular weight at a given film thickness (∼80 nm). Moreover, Fuchter and co-workers[33] used 53% of 1-aza[6]helicene to achieve a gabs of 0.2 for achiral F8BT, whereas we could reach similar gabs values at only 8–10 wt % of PEM-OH for c-PFBT. It was also observed that at low loading of PEM-OH (<10 wt %) the films were macroscopically uniform without affecting any of the photophysical properties of the pristine polymers.

Outlook and Conclusion

Here we have developed a method to improve the chiroptical properties in the thin-films of enantiopure conjugated polymers using a commercially available achiral long-chain alcohol (PEM-OH) as an additive. The enhancement in chiroptical properties is ca. 5–10 times in the annealed thin-films and is applicable to a broad range of enantiopure conjugated polymers. Based on microscopic studies, we attribute the enhancement in chiroptical properties to improved chiral liquid crystalline ordering of polymer chains on addition of PEM-OH. We envisage that the PEM-OH acts as a supramolecular plasticizer which aids in providing increased mobility to the polymer chains beyond Ttrans or Tm, thereby improving their chiral liquid crystalline organization. PEM-OH can be viewed as a processing agent to enhance chiroptical properties, analogues to the alkane di(thiol/iodide) which are widely used additives to enhance the efficiency of organic solar cells.[37,38]

We have identified the following criteria to be crucial for the PEM-OH methodology to work: (i) the chiral self-assembly of the enantiopure conjugated polymers in alcohols as solvent is a prerequisite to using the PEM-OH method in the thin-film, and (ii) in principle this methodology could work with other long-chain alcohols with appropriate thermal behavior (Tm, alcohol < Ttrans, polymer/Tm, polymer and that the alcohol additive remains in the molten state at the Ttrans or Tm of the polymer). Since PEM-OH is a disperse polymer, it would be interesting to investigate the effect of the dispersity of the long-chain alcohol additive on the chiroptical enhancement. We anticipate that this new class of UV–vis–NIR transparent long-chain alcohol additives which does not affect the photophysical properties of the conjugated polymers will pave the way for harnessing the chirality of enantiopure conjugated polymers for various applications.

Methods

Sample Preparation for PEM-OH Blended Films

A stock solution of PEM-OH at a concentration of 1 mg/mL was prepared by dissolving the required amount of freshly powdered PEM-OH (as obtained from Sigma-Aldrich) in chloroform as the solvent in a vial with PTFE seal cap (Note 1). The sealed vial containing PEM-OH and chloroform was heated at 70 °C (oil bath temp) for 2 h to ensure complete dissolution of PEM-OH in chloroform. The vial was further sonicated for 5 min and heated with a heat gun. Separate vials (1.5 mL) containing ∼1.5–1.7 mg of the polymer were charged with different amounts of the semihot PEM-OH stock solution (Note 2). The chloroform from each of the sample vials was evaporated by gently blowing N2 gas and finally heating with heat gun to ensure complete removal of the solvent. To each of the sample vials, fresh chloroform was added such that the concentration of the sample with respect to the polymer was 15 mg/mL (Note 3). These vials were further heated on an oil bath at 70 °C for 2 h to ensure the homogeneous mixing of the polymer and PEM-OH. The samples once cooled down to room temperature were spin-coated (2000 rpm, 60 s, maximum acceleration) on clean glass slides. The slides were further annealed beyond the Ttrans or Tm of the polymers in a glovebox for 15 min. All the spectra are recorded at room temperature (20 °C).

Note 1: It is important to freshly powder the commercially available PEM-OH pallets instead of using powdered and stored PEM-OH. The extent of chirality enhancement was found to be low with stored powder. Also it was observed that powdered and stored PEM-OH was difficult to dissolve in chloroform using the above-described procedure. We think it is mostly due to the hygroscopic nature of the PEM-OH, which might result in powdered sample adsorbing water and making it difficult to dissolve in chloroform and consequently affecting the enhancement factor.

Note 2: By semihot we mean at a temperature of around 30–40 °C. By allowing the PEM-OH stock solution to cool down to room temperature, we saw a white precipitate. Thus, PEM-OH may not be completely soluble in chloroform at room temperature.

Note 3: The concentration was with respect to the amount of polymer taken and not with respect to the total amount of the material (polymer + PEM-OH). This is because, by considering the concentration with respect to the total material (polymer + PEM-OH), the magnitude of Cotton effect decreases at higher weight percentage of PEM-OH due to lowering of polymer concentration.