# Unidirectional Perpendicularly Aligned Lamella-Structured Oligosaccharide (A) ABA Triblock Elastomer (B) Thin Films Utilizing Triazolium + /TFSI – Ionic Nanochannels

Johanna Majoinen, Cécile Bouilhac, Patrice Rannou, Redouane Borsali

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Johanna Majoinen, Cécile Bouilhac, Patrice Rannou, Redouane Borsali. Unidirectional Perpendicularly Aligned Lamella-Structured Oligosaccharide (A) ABA Triblock Elastomer (B) Thin Films Utilizing Triazolium + /TFSI – Ionic Nanochannels. ACS Macro Letters, 2022, 11 (1), pp.140-148. 10.1021/acsmacrolett.1c00712. hal-03514163

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Submitted on 30 May 2022

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# Unidirectional Perpendicularly Aligned Lamella-Structured Oligosaccharide (A) ABA Triblock Elastomer (B) Thin Films Utilizing Triazolium⁺/TFSI⁻ Ionic Nanochannels

Johanna Majoinen,* Cécile Bouilhac, Patrice Rannou,* and Redouane Borsali*

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Cite This: ACS Macro Lett. 2022, 11, 140–148

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Supporting Information

**ABSTRACT:** We designed and synthesized high $\chi$-low N-maltoheptaose-(triazolium⁺/N(SO₂CF₃)₂⁻)-polyisoprene-(triazolium⁺/N(SO₂CF₃)₂⁻)-maltoheptaose ABA triblock elastomers featuring triazolium⁺/N(SO₂CF₃)₂⁻ (TFSI⁻) counteranion ionic interfaces separating their constituting polymeric sub-blocks. Spin-coated and solvent-vaporAnnealed (SVA) MH₁.₂k-(T⁺/TFSI⁻)-PI₄.₃k-(T⁺/TFSI⁻)-MH₁.₂k thin films demonstrate interface-induced charge cohesion through ca. 1 nm “thick” ionic nanochannels which facilitate the self-assembly of a perpendicularly aligned lamellar structure. Atomic force microscopy (AFM) and (grazing-incidence) small-angle X-ray scattering ((GI)-SAXS) characterizations of MH₁.₂k-(T⁺/TFSI⁻)-PI₄.₃k-(T⁺/TFSI⁻)-MH₁.₂k and pristine triBCP analogous thin films revealed sub-10 nm

block copolymer (BCP) self-assembly and unidirectionally aligned nanostructures developed over several $\mu$m² areas. Solvated TFSI⁻ counterions enhance the oligosaccharide sub-block packing during SVA. The overall BCP phase behavior was mapped through SAXS characterizations comparing di- vs triblock polymeric architectures, a middle PI sub-block with two different molecular masses, and TFSI⁻ or I⁻ counteranion effects. This work highlights the benefits of inducing single-point electrostatic interactions within chemical structures of block copolymers to master the long-range self-assembly of prescribed morphologies.

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Synthetic block copolymers (BCPs) are key enabling building blocks toward functional organic materials with tunable-by-design properties.¹ Hierarchical self-assembly of tailored-made macromolecular architectures into prescribed morphologies (featuring cylinders, lamellae, spheres, etc.)² with desired functions becomes experimentally facile when fine-tuning the polymer-polymer interactions (Flory-Hugins parameter, $\chi$) for highly immiscible blocks and their volume fractions ($f$) with an adjusted number of repeating units (N). Traditional coil-coil BCP nanostructures with a domain spacing of tens of nanometers (nm) have paved the way toward the so-called high $\chi$-low N BCPs to obtain smaller features, down to the sub-10 nm dimensions.³ Within high $\chi$-low N BCPs, the sub-blocks have high immiscibility⁴ and small N values resulting in nanostructures featuring domain sizes as small as 3 nm, highly sought for nanopatterning applications.⁵,⁶ Oligosaccharides function simultaneously as sustainable and key-enabling high $\chi$ building blocks to allow for sub-10 nm BCP domain sizes.⁷⁻¹¹ Moreover, oligosaccharide-based BCPs can be elegantly synthesized with ready-made synthetic building blocks utilizing the copper(I)-catalyzed alkyne-azide cycloaddition (CuAAC) click reaction.¹²,¹³

We designed and synthesized high $\chi$-low N maltoheptaose (MH) and polyisoprene (PI) block coelastomers using CuAAC coupling to target triazole junction point function-

ality.¹⁴ The MH vs PI sub-block's high polarity difference leads to high immiscibility and hence high $\chi$.¹⁵ The flexible PI sub-block consists of an ideal complementary block for BCP processing through providing a soft matrix. In addition to the influence of $\chi$ and $f$, supramolecular interactions (e.g., $\pi$-π stacking,¹⁶ hydrogen bonding,¹⁷ and ionic interactions¹⁸,¹⁹) at the BCP interface have recently demonstrated compelling evidence for enhanced self-assembly, ionic interactions notably inducing unique counterion effects.¹⁹ Ionically conducting BCP thin films with controlled structure orientation (perpendicular or parallel) with respect to electrodes are highly sought in order to allow for efficient anisotropic ionic transport.²⁰ To date, BCP domain orientation in thin films relies on mastering the subtle interplay of varying energies at polymer-air, polymer-polymer, and polymer-substrate interfaces.²¹ To address this issue, we report on the effect of electrostatic interactions at charge-modified BCP interfaces to control the self-assembly of oligosaccharide-based high $\chi$-low

Received: November 13, 2021

Accepted: December 28, 2021

Published: January 3, 2022

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<figure><img src="image_9.png" /><figcaption>Scheme 1. Synthesis (a) of a Charge-Modified ABA Maltoheptaose-(triazolium⁺/counteranion⁻)-Polyisoprene-(triazolium⁺/counteranion⁻)-Maltoheptaose triBCP with End-Functionalized Maltoheptaose and Polyisoprene Building Blocks Using CuAAC Click Chemistry Coupling and Subsequent *n*-Alkylation of Triazole (T) Junction Units and (b) Schematics for Charge-Modified triBCP Interfaces in Self-Assembled Thin Films with a Perpendicular Lamella-Based Nanostructure and Ionic Nanochannels</figcaption></figure>

N BCPs. $MH_{1.2k}^-(triazolium^+/TFSI^-)-PI_{4.3k}^-(triazolium^+/TFSI^-)-MH_{1.2k}$ triBCP thin films were prepared accordingly, wherein the formation of ionic nanochannels guides the BCP structure orientation (Scheme 1). Generally, controlling the orientation of BCP structures from several $\mu m^2$ up to the cm² range is realized with the help of shearing²² and external fields²³ (e.g., electric or magnetic) or through templating.²⁴ Here, we show how charge cohesion of the BCP interfaces promotes unidirectional perpendicular lamella (Lam) nano-structure formation over areas of several $\mu m^2$ for solvent-vapor-annealed²⁵,²⁶ (SVA) BCP thin films. We provide a direct vs reciprocal space quantification of sub-10 nm Lam domain spacing (d) in thin films with atomic force microscopy (AFM) imaging and grazing-incidence small-angle X-ray scattering (GISAXS), respectively.

Ready-made MH (highly discrete number-average molar mass $M_n$ distribution, with $M_n$ = 1.2 kg mol⁻¹: Figure S1) and hemitelechelic α-monohydroxy-end-capped ($M_n$ = 3.6 kg mol⁻¹) and homotelechelic α,ω-bishydroxy-end-capped PIs ($M_n$ = 4.3 kg mol⁻¹ and $M_n$ = 9.0 kg mol⁻¹, respectively) were end-functionalized and further used in the synthesis of AB diBCPs and ABA triBCPs through CuAAC (Scheme 1). Coupling reaction conditions and polymer characterizations are described in the Supporting Information (SI) (Figures S2–S8). The reducing chain end of MH was selectively functionalized with an alkyne moiety, using propargyl

amine.²⁷ PIs ($D = M_w/M_n$ = 1.09–1.25) were modified with 6-azido-hexanoic acid to afford end-functionalized elastomer sub-blocks with an azide function. CuAAC yielded $MH_{1.2k}^-(triazole)-PI_{3.6k}$ diBCP and $MH_{1.2k}^-(triazole)-PI_{4.3k/9k}^-(triazole)-MH_{1.2k}$ triBCP model compounds with 1,2,3-triazole (T) junction units (Table S1 for polymer properties). Finally, a straightforward route to the BCP ionic interface is demonstrated by *n*-alkylation of triazole ring(s) with *N*-methyl bis[(trifluoromethyl)sulfonyl]imide (MeTFSI) or iodomethane (MeI), creating a methyltriazolium ($T^+$)/counteranion⁻ ($TFSI^-$ or $I^-$) junction separating the sub-blocks. Full conversion of T junctions to $T^+/TFSI^-$ using MeTFSI was verified with ¹H NMR spectroscopy (Figures S9 and S10). N-Alkylation with MeI did not reach full conversion, even with prolonged reaction times, ambient temperature, or an extra amount of reagent (Figures S9 and S11). The $T^+/I^-$ interface is thermally unstable, resulting in N-demethylation.²⁸ Moreover, MeI reacts with PI double bonds by coordination bonding, even covalently,²⁹ reducing the triazole-to-methyl-triazolium ($T$-to-$T^+$) conversion. The results related to MeI are therefore presented here as a normative base for comparing effects of the counterion ($TFSI^-$ or $I^-$) onto BCP self-assembly.

BCP glass transition temperatures ($T_g$) were determined with differential scanning calorimetry (DSC) (Figures S12–14 and Table S1). $T_g$ values varied in between 5 and 19 °C for
<figure><img src="image_10.png" /><figcaption>**Figure 1.** Selected data (including *d* = 2π/q values) from variable-temperature SAXS characterizations (heating scan from 25 to 185 °C followed by a cooling scan down to 25 °C) of pristine (neutral T unit) (a) and charge-modified (T⁺/TFSI⁻ or T⁺/I⁻ junction units) (b,c) diBCPs, (d–f) triBCPs with 4.3 kg mol⁻¹ for the PI middle block, and (g–i) triBCPs with 9.0 kg mol⁻¹ for the PI middle block.</figcaption></figure>

pristine and charge-modified BCPs. PI backbone structures rich in 1,2- and 3,4-addition typically have higher T~g~ values than PIs exhibiting only 1,4-structure.³⁰ Thermal transitions observed during the first heating scan could not be reproduced during the second cycle for any of the BCPs studied. Order–disorder transition temperature (T~ODT~) for MH-based BCPs with high χ is expected to be high, possibly unobtainable before triggering the BCP thermal degradation. Further annealing steps during DSC measurements below BCP T~ODT~ were not performed in order to avoid their chemical degradations.³¹

Variable-temperature SAXS characterizations for all di- and triBCPs were performed to quantify the effect of thermal treatment on nanostructure formation for the investigated polymer architectures (Figure 1). We discuss the effect of the counteranion on phase behavior and, additionally for pristine vs charge-modified triBCPs, the effect of two different M~n~ values for the PI middle sub-block.

The downsizing effect of thermal treatment onto the domain spacing (*d*) for charge-modified BCPs is evident from the comparison of the primary scattering peak (*q*\*) positions after

heating (Figure 1b, c, e, f, h, i; dashed vertical lines). Pristine di- and triBCP *q*\* positions remain unchanged and with a broad profile (Figure 1a, d, g). A clear enhancement for the hexagonally packed cylinder (Hex) morphology is observed in SAXS profiles for MH<sub>1.2k</sub>-(*T*<sup>+</sup>/TFSI<sup>-</sup>)-PI<sub>3.6k</sub> and MH<sub>1.2k</sub>-(*T*<sup>+</sup>/I<sup>-</sup>)-PI<sub>3.6k</sub> diBCPs with Bragg reflections (Figure 1b,c) displaying *q*/*q*\* ratios: 1, √3, 2, √7, and √12. MH cylinders in the PI matrix are indicated with *f*<sub>PI</sub> = 86.<sup>15</sup> MH<sub>1.2k</sub>-(*T*<sup>+</sup>/TFSI<sup>-</sup>)-PI<sub>3.6k</sub> with the *T*<sup>+</sup>/TFSI<sup>-</sup> junction has a reduced *d* = 12 nm compared to the pristine diBCP (*d* = 14 nm) (Figure 1a,b). The Hex phase evolves between 150 and 180 °C for both charge-modified diBCPs. Interestingly, MH<sub>1.2k</sub>-(*T*<sup>+</sup>/I<sup>-</sup>)-PI<sub>3.6k</sub> and pristine diBCP Hex morphologies present the same *d* values. *d* remains unaffected possibly because of partial T-to-T<sup>+</sup>/I<sup>-</sup> conversion, leading to incomplete ion connectivity between the interfaces.

The charge-modified MH<sub>1.2k</sub>-(*T*<sup>+</sup>/TFSI<sup>-</sup>)-PI<sub>4.3k</sub>-(*T*<sup>+</sup>/TFSI<sup>-</sup>)-MH<sub>1.2k</sub> and MH<sub>1.2k</sub>-(*T*<sup>+</sup>/I<sup>-</sup>)-PI<sub>4.3k</sub>-(*T*<sup>+</sup>/I<sup>-</sup>)-MH<sub>1.2k</sub> triBCPs both show the Lam morphology at 170 °C, with a considerable decrease of *d* of ca. 5 nm when compared to pristine MH<sub>1.2k</sub>-(*T*<sup>+</sup>)-PI<sub>4.3k</sub>-(*T*<sup>+</sup>)-MH<sub>1.2k</sub> with *d* = 16 nm (Figure
<figure><img src="image_11.png" /><figcaption>**Figure 2.** AFM height images for (a) charge-modified $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{4.3k}^{+}(T^{+}/TFSI^{-})-MH_{1.2k}$ versus (c) pristine $MH_{1.2k}^{+}(T)-PI_{4.3k}^{+}(T)-MH_{1.2k}$ triBCP thin films. Fast Fourier transforms (FFTs) associated with an AFM topography image are used in image filtering in (b) and (d) presented with a *difference* image of filtered data and a *filtered* data image to clarify the unidirectional vs local line orientation between the two films.</figcaption></figure>

1d–f). The $MH_{1.2k}^{+}(T^{+}/I^{-})-PI_{4.3k}^{+}(T^{+}/I^{-})-MH_{1.2k}$ analogue preserves the long-range order with decreased *d* after heating. Compared to diBCPs, the ABA triBCP architecture with polydisperse middle B block can experience packing frustrations during phase transition.³² Exemplifying this phenomenon, pristine triBCP with a dispersed ($D = 1.25$) $PI_{4.3k}$ middle block and $f_{PI} = 78$ resulted in a Hex phase with a curved interface. Counterion mobility and solubility can either suppress or enhance BCP nanostructure formation,³³ with confined counterions at the interface possibly suppressing phase separation as a consequence of an entropic penalty. TriBCPs with the $PI_{9.0k}$ middle block ($D = 1.09$) and $f_{PI} = 88$ form Hex phases regardless of the counterion, yet with a smaller *d* for $MH_{1.2k}^{+}(T)-PI_{9k}^{+}(T)-MH_{1.2k}$ compared to the $T^{+}/TFSI^{-}$ interface triBCP supporting the effects of middle-block dispersity on phase separation (Figure 1d,g). $MH_{1.2k}^{+}(T^{+}/I^{-})-PI_{3.6k}$, $MH_{1.2k}^{+}(T^{+}/I^{-})-PI_{4.3k/9.0k}^{+}(T^{+}/I^{-})-MH_{1.2k}$ diBCP, and triBCP SAXS data illustrate that T-to-T<sup>+</sup>/I<sup>-</sup> full conversion is needed neither to achieve long-range order (Figure 1c, f, i) nor to decrease the *d*. The bulky TFSI<sup>-</sup> counterion can disrupt block-block interactions restraining crystallization for rod-coil BCPs.¹⁹ Similar disturbed interactions are evidenced in $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{4.3k}^{+}(T^{+}/TFSI^{-})-MH_{1.2k}$ and $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{9k}^{+}(T^{+}/TFSI^{-})-MH_{1.2k}$ SAXS data, as MH hydrogen bonding and T<sup>+</sup>/TFSI<sup>-</sup> interface interactions hamper the phase transition (Figure 1e,h). Pristine $MH_{1.2k}^{+}(T)-PI_{9k}^{+}(T)-MH_{1.2k}$ higher-order reflections appeared on reheating to 185 °C, but the primary scattering peak (*q**) remained broad and of low intensity after heating, indicating a rather disordered final nanostructure (Figure 1g).

As the effect of the $T^{+}/TFSI^{-}$ interface on enhancing the triBCP bulk self-assembly seemed moderate according to variable-temperature SAXS, we next focused our attention on thin film self-assembly and solvent vapor annealing (SVA). AFM was used to image $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{4.3k}^{+}(T^{+}/TFSI^{-})-MH_{1.2k}$ and $MH_{1.2k}^{+}(T)-PI_{4.3k}^{+}(T)-MH_{1.2k}$ triBCP thin films prepared by spin-coating on plasma-treated silicon wafers (see details in the SI). To assess the effect of the $T^{+}/TFSI^{-}$ interface on thin film morphology and structure orientation related to the substrate surface, the BCP film thickness, substate surface energy, and SVA time with solvent composition used were kept constant throughout the experiments. SVA was performed in a closed container for 24 h using a THF/H₂O 90:10 wt % solvent mixture placed next to the thin film. A film thickness of ca. 21 nm after SVA was
<figure><img src="image_12.png" /><figcaption>**Figure 3.** AFM height analyses of $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ thin films ($5~\mu m^2$ area). Zoom-in images numbered 1–4. Image 4 shows a defect edge, where uniaxial lines appear perpendicular to each other.</figcaption></figure>

determined with AFM from film scratch height. As-cast $MH_{1.2k}^{+}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ and $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin films displayed an initial disordered surface topography (Figure S18). After SVA, the differences in the film topographical features became highly salient (Figure 2). As the pristine $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin film fingerprint lines align locally, forming small-size granular domains (highlighted in Figure 2c,d with circles), the charge-modified $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ thin film features unidirectionally aligned lines across the image (Figures 2a,b and S16), over distances of 500 nm. The line spacing (L) extracted from FFTs indicated a *d* value of 11 nm ($L$ = 5.5 nm) for $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ and *d* value of ca. 14 nm for $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ ($L$ varies between 6.6 and 7.4 nm) (Figure 2a,c). The $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ thin film lines appear hazy (Figure 2a). 3D visualization of a $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ thin film height image shows a surface roughness of ca. 4 nm, as the higher surface energy PI block protrudes at the air–polymer surface (Figure S15). Nanostructure orientations are highlighted with 2D FFT filtering (Gwyddion software) (Figure 2b,d). Filtered separated data (difference image in Figure 2b inset) reveal clear bright/dark alternating lines. Applying the same filtering procedure for areas in the ellipsoidal FFT profile of the $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin film allows distinguishing the local granular domain alignment (red and blue circles in Figure 2d) with varying line orientations (red and blue arrows Figure 2d).

Figure 3 further confirmed that the $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ thin film unidirectional line orientation extends up to the $5~\mu m^2$ area. Curiously, careful AFM imaging revealed minority areas with hexagonal arrays of isolated dots on the surface complicating the structure interpretation (Figures 3, image 4, and S17).

GISAXS characterizations confirmed the morphologies for $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ and $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin films (Figure 4). Charge-modified triBCP showed a clear in-plane Lam scattering pattern ($q^* = 0.6, 2q^* = 1.2$) with a $d_{charged}$ value of 10.5 nm (Figure 4a,b). Whereas sharp spots are clearly seen at the in-plane Yoneda line for the $T^{+}/TFSI^{-}$ interface (Figure 4a,b), a pristine $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin film displays broad peaks with Debye–Scherrer rings (pointed with arrows in Figure

$4d,e)$ attributed to the tilted domain orientations within the thin film.34 A Lam nanostructure is also obtained for the $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin film ($q^* = 0.48, 2q^* = 0.95$) with $d_{neutral} = 13$ nm (Figure 4e) in full agreement with AFM analyses. Intense rod-shaped out-of-plane reflections are seen for both pristine and charge-modified thin films (Figure 4a and c and 4d and f). These Bragg rods result from incident beam reflection from an ultrathin BCP film where the perpendicular Lam nanostructure is aligned parallel with respect to the reflected beam35 (schematics Figure 4a). The charge-modified triBCP thin film produces a sharp and narrow Bragg rod compared to the broad and somewhat distorted one shown by the pristine triBCP thin film due to Debye–Scherrer rings distorting the rod reflections (Figure 4a,c and 4d,f). GISAXS data for as-cast $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ and $MH_{1.2k}^{-}(T)-PI_{4.3k}^{-}(T)-MH_{1.2k}$ thin films did not show notable structure development. (Figure S18). Evidence for the Hex phase formation in thin films was not observed with GISAXS. We therefore conclude on Lam structure formation for $MH_{1.2k}^{-}(T^{+}/TFSI^{-})-PI_{4.3k}^{-}(T^{+}/TFSI^{-})-MH_{1.2k}$ both in bulk and for the thin film, regardless of $f_{PI} = 78$ (Figure 1e and 1a–c). The AFM imaging of a grain boundary with merged facing line frontiers (Figure S16) supports the claims that dotted features (Figures 3 image 4 and S17) are nonequilibrium structures within a swollen BCP thin film. This is also compatible with dispersity-induced $PI_{4.3k}$ middle-block packing frustrations which affect the evolution of the surface morphology.32

Oligosaccharide-based BCPs are highly responsive to SVA7 and microwave annealing.36 Modeling studies have revealed that the solvation of the $TFSI^−$ counteranions with water molecules is imparted by strong hydrogen-bonding interactions37 and $TFSI^−$ anions contributing to the nanophase segregation process at play within thin films of MH-based triBCPs. Tetrahydrofuran promotes the mobility of the PI sub-block during SVA, while minute amounts of water facilitate interactions of $TFSI^−$ with MH sub-blocks. Importantly, the THF/water mixture offers a neutral top layer for both MH and PI sub-blocks to emerge at the polymer-THF/water interface, promoting an equilibrium Lam formation, possibly transiting through a perpendicular Hex top layer structure before stabilizing into a final perpendicularly aligned Lam38 (Figure 3 and S17).
<figure><img src="image_13.png" /><figcaption>**Figure 4.** GISAXS results: (a) 2D SAXS pattern recorded for a $MH_{1.2k}^{+}$(T+/TFSI⁻)-PI$_{4.3k}^{+}$(T+/TFSI⁻)-$MH_{1.2k}$ thin film combined with a scheme showing the X-ray beam configuration with respect to the Lam nanostructure. (b,c) In-plane vs out-of-plane corresponding 1D scattering profiles. (d) 2D SAXS pattern acquired onto a $MH_{1.2k}^{+}$(T)-PI$_{4.3k}^{+}$(T)-$MH_{1.2k}$ thin film. Note that out-of-plane regions are indicated with yellow dashed lines and Debye-Scherrer rings highlighted with a white arrow. (e,f) In-plane vs out-of-plane corresponding 1D scattering profiles.</figcaption></figure>

The $MH_{1.2k}^{+}$(T+/TFSI⁻)-PI$_{4.3k}^{+}$(T+/TFSI⁻)-$MH_{1.2k}$ Lam nanostructure depends on the ca. 21 nm thin film thickness (t), which is commensurate with the $d_{charged} = 10.5$ nm of the Lam ($t/d_{charged} = 2$). We suggest that strong electrostatic interactions of T+/TFSI⁻ trigger the self-assembly of well-connected channels, enabling the unidirectional Lam alignment with a 2.5 nm decrease in d, regardless of the high $f_{PI}$ (Figure 5). Luo et al. reported on locally aligned structures for thermally annealed and reactive ion-etched PDMS$_{1.7k}$-b-PMMA$_{5.1k}$ thin films, unaffected by the presence of an ionic junction interfacing the PDMS and PMMA sub-blocks.¹⁸ Vice versa, Ji et al. reported on poly(3-hexylthiophene) amorphization due to a T+/TFSI⁻ interface hampering with rod-block π-π interactions upon thermal annealing of poly(3-hexylth-

iophene)-b-poly(methyl methacrylate).¹⁹ As we rely on a thin film thickness commensurate with the domain spacing (*vide supra*) and SVA for enhancing TFSI⁻ mobility, the electrostatic interactions prevail, leading to well-connected T+/TFSI⁻ interfacial ionic nanochannels. To the best of our knowledge, this is the first report of a long-range unidirectional alignment for a BCP Lam nanostructure induced by electrostatic interactions within ionic nanochannels defined by T+/counter-anion⁻ junctions separating polymeric sub-blocks. We emphasize on utilizing SVA with optimized BCP film thicknesses to enable strong electrostatic interactions within ionic nanochannels to result in long-range aligned microphase-separated morphologies. Increasing the $f_{PI}$ $M_n$ to 9.0 kg mol⁻¹ in triBCP thin film indicates the formation of a Hex phase
<figure><img src="image_14.png" /><figcaption>**Figure 5.** Suggested effects of (a) charged interface (T⁺/TFSI⁻)-induced charge cohesion for the self-assembly of MH₁.₂k⁻(T⁺/TFSI⁻)-PI₄.₃k⁻(T⁺/TFSI⁻)-MH₁.₂k triBCP thin films and of (b) a neutral (T) interface for the self-assembly of MH₁.₂k⁻(T⁻)-PI₄.₃k⁻(T⁻)-MH₁.₂k triBCP thin films. Charged T⁺/TFSI⁻ junction units self-assembled into ionic nanochannels promoting stong interactions among MH sub-blocks, while T interfaces are less effective, leading to irregular interactions between MH sub-blocks. The ionic connectivity is schematically illustrated with triazolium (T⁺) rings in yellow versus TFSI⁻ counteranions in gray.</figcaption></figure>

(Figure 1g,h,i) and requires rebalancing the surface energies for the successful formation of ionic nanochannels.

To summarize, we show how one can leverage copper(I)-catalyzed alkyne-azide cycloaddition (CuAAC) click chemistry and *n*-alkylated triazolium⁺/counteranion⁻ junctions to enhance the bulk and thin film self-assembly of high *χ*-low *N* diblock and triblock copolymers using maltoheptaose (MH) and polyisoprene (PI) sub-blocks. Full T-to-T⁺/TFSI⁻ conversion is obtained using MeTFSI in *n*-alkylation. Interestingly, despite conversion as low as 11% for T-to-T⁺/I⁻, SAXS studies confirmed enhanced BCP microphase separation, illustrating the powerfulness of T⁺/counteranion⁻ junctions to fine-tune BCP self-assembly. TFSI⁻ solubilization during SVA of the BCP thin film together with optimized film thickness enable long-range-ordered unidirectional perpendicular Lam formation, quantified for MH₁.₂k⁻(T⁺/TFSI⁻)-PI₄.₃k⁻(T⁺/TFSI⁻)-MH₁.₂k thin film with both real-space (AFM) and reciprocal-space (GISAXS) analyses. Large areas of several *µm*² featuring sub-10 nm charge-modified triBCP domains are remarkably uniform and easily fabricated. Long-range nanostructure orientation is conveniently achieved without shearing or relying on graphoepitaxy, highlighting how electrostatic interactions facilitate BCP domain alignment through ionic nanochannel formation. Considering the library of BCPs accessible through CuAAC click chemistry of hemitelechelic and homotelechelic synthetic or biosourced/based polymeric building blocks, thereby amenable to *n*-alkylation of triazole junction units, this study opens doors to explore long-range ordered BCP thin films for advanced nanopatterning (nanoelectronics) or efficient and dimensionality-controlled ionic transport for electrochemical energy storage (nanoionics).

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## ASSOCIATED CONTENT

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### Supporting Information

The Supporting Information is available free of charge at
https://pubs.acs.org/doi/10.1021/acsmacrolett.1c00712.

Individual polymer block analyses (Maldi-ToF mass spectrometry), BCP syntheses and characterizations (¹H NMR, FT-IR), DSC, additional AFM images, and GISAXS analyses (PDF)

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## AUTHOR INFORMATION

### Corresponding Authors

Johanna Majoinen – Université Grenoble Alpes, CNRS, CERMAV, 38000 Grenoble, France; Université Grenoble Alpes, CNRS, CEA, INAC-SyMMES, 38000 Grenoble, France; Present Address: Department of Bioproducts and Biosystems, Vuorimiehentie 1, P.O. Box 16300, FI-00076 Aalto University, Finland; orcid.org/0000-0001-8941-2797; Email: johanna.majoinen@aalto.fi

Patrice Rannou – Université Grenoble Alpes, Université Savoie Mont Blanc, CNRS, Grenoble INP, LEPMI, 38000 Grenoble, France; Université Grenoble Alpes, CNRS, CEA, INAC-SyMMES, 38000 Grenoble, France; Email: patrice.rannou@grenoble-inp.fr

Redouane Borsali – Université Grenoble Alpes, CNRS, CERMAV, 38000 Grenoble, France; Email: redouane.borsali@cermav.cnrs.fr

### Author

Cécile Bouilhac – ICGM, Université Montpellier, CNRS, ENSCM, 34095 Montpellier, France; orcid.org/0000-0002-1898-2570

Complete contact information is available at:
https://pubs.acs.org/10.1021/acsmacrolett.1c00712
## Author Contributions

The manuscript was written through contributions of all authors. All authors have given approval to the final version of the manuscript.

## Notes

The authors declare no competing financial interest.

## ACKNOWLEDGMENTS

Supported by the “Emergence and Strategic Partnership” funding granted by Université Joseph Fourier (UJF) under the “BiotriCo” project, this work has been performed at Université Grenoble Alpes (France) and at Aalto University (Finland). Additional partial support by the Polynat Carnot Institute (No. 16-CARN-025-01) is greatly acknowledged. We thank the ESRF synchrotron facility for beamtime allocation at the BM02-D2AM French CRG beamline (WOS funded by the French National Research Agency (ANR) “Investissements d’avenir” program, grant number: ANR-11-EQPX-0010). We express our gratitude to Nathalie Boudet and Isabelle Morfin for assistance during data acquisition and their processing at the BM02-D2AM French CRG beamline. Johanna Majoinen acknowledges financial support from Emil Aaltonen Foundation and Fortum Foundation Finland. Cécile Bouilhac, Patrice Rannou, and Redouane Borsali acknowledge supports from the Centre National de la Recherche Scientifique (CNRS) at UMR5253-ICGM, at UMR5279-LEPMI and UMR5819-SyMMES, and at UPR5301-CERMAV laboratories. We also thank Olli Ikkala, Sami Halila, and Yoshihura Nishiyama for insightful discussions.

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