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Reversible conformation-driven order–order transition of peptide-mimic poly(n-alkyl isocyanate) in thin films via selective solvent-annealing


We report for the first time the conformational and structural details of peptide-mimic poly(n-hexyl isocyanate) (PHIC). PHIC is a representative poly(n-alkyl isocyanate)s, which have received significant attention because of their unique stiff chain characteristics and potential applications in various fields. A well-ordered hexagonal close packing structure of PHIC with 83 helical conformation was clearly observed in the nanoscale thin films that were selectively annealed with carbon disulfide (CS2). A well-ordered multi-bilayer structure of the polymer with β-sheet conformation was also clearly formed in the films that were selectively annealed with toluene. In addition, a fully reversible transformation between these two self-assembled structures was demonstrated by consecutive annealings with CS2 and toluene.


Poly(n-alkyl isocyanate)s (PAICs) have received considerable attention as helical, stiff, rod-like polymers because of their unique characteristics and structural features, which include their large persistence length (20–60 nm) and their potential applications in chiral recognition, optical switches, liquid crystals, degradable materials and composites.1, 2, 3, 4, 5, 6, 7, 8 Considerable research efforts have been dedicated to improving the understanding of the conformation and packing of PAICs. Specifically, poly(n-butyl isocyanate) (PBIC) and poly(n-hexyl isocyanate) (PHIC) (Figure 1a) have been thoroughly investigated as representative PAICs. Despite these extensive studies, however, the conformation and molecular packing of PAICs have yet to be unequivocally established. For example, several helical conformations have been proposed, namely 21, 51 and 83 in solution9, 10, 11, 12 and 83, 85 and 125 in the solid state.13, 14, 15 Furthermore, triclinic, monoclinic and pseudo-hexagonal lattices have all been proposed as possible molecular packing structures.13, 14, 16

Figure 1
figure 1

Two-dimensional (2D) GIXS patterns measured at αi=0.150° for thin films of PHIC (A) deposited onto silicon substrates: (a) as-cast; (b) CHCl3-annealed for 3 h.

In the present work, we provide the first report on the formation of PHIC in thin films with both a helical conformation-based hexagonal packing order and a β-sheet conformation-based lamellar structure; we also demonstrate the complete reversibility of the order–order phase transition under selective solvent annealing.

Materials and methods

Materials and PHIC synthesis

PHIC was synthesized from n-hexyl isocyanate using living anionic polymerization based on a method reported in the literature.17, 18 n-Hexyl isocyanate (HIC, 97%, Aldrich, Milwaukee, WI, USA) was dried over CaH2 and distilled under vacuum. An initiator, sodium benzanilide (Na-BA) in tetrahydrofuran (THF, 50 ml), was prepared from the reaction of equivalent amounts of benzanilide (8.70 g, 0.043 mol) and elemental sodium (1.00 g, 0.043 mol) at room temperature. The polymerization reactions of HIC were conducted under high vacuum in a glass apparatus equipped with break-seals. In a typical procedure, the initiator solution, Na-BA (0.013 g, 0.066 mmol) in THF, was transferred into the reaction flask through the break-seal, and the solution temperature was then equilibrated to the reaction temperature of −98 °C. The polymerization was initiated by adding the HIC monomer (0.753 g, 5.93 mmol) in THF to the initiator solution. The reaction was terminated after 60 min by adding a 20-fold excess of HCl in methanol when the target PHIC product was precipitated. The PHIC precipitates were filtered off and dried in vacuo. The methanol soluble portion was determined quantitatively by weighing the residue after evaporation of methanol and using proton nuclear magnetic resonance spectroscopy to determine whether any unreacted monomers and/or trimers were present. The yield of the polymer was 99%. The obtained PHIC product was characterized using both proton and carbon nuclear magnetic resonance (1H and 13C NMR) spectroscopies with a JEOL NMR spectrometer (model JNM-LA300WB, JEOL Ltd, Tokyo, Japan) and using Fourier transform infrared (FT-IR) spectroscopy with a Perkin Elmer spectrometer (model 2000, Perkin Elmer, Waltham, MA, USA). PHIC 1H NMR (CDCl3, 300 MHz), δ (p.p.m.): 0.9 (3H, CH3), 1.0–2.0 (8H, (CH2)4), 3.7 (2H, N-CH2-) (Supplementary Figure S1). 13C NMR (CDCl3, 75 MHz), δ (p.p.m.): 14.5 (CH3), 22.5 (CH2), 26.2 (CH2), 28.5 (CH2), 31.5 (CH2), 48.6 (N-CH2-), 156.8 (C=O) (Supplementary Figure S2). IR (KBr, cm−1): 3441 (-NH), 2959, 2932, 2860 (CH2), 1700 (C=O), 1349/1297 (disubstituted amide), 1227, 1175, 1092, 785, 728 (CH2).

The molecular weights of the polymers were determined using a multi-angle laser light scattering detector system and a size exclusion chromatography system (Interferometric Refractometry 478-009-690, Optilab DSP, Phoeix, AZ, USA and DAWN EOS Laser Photometer 113-E, Wyatt Technology, Santa Barbara, CA, USA) with four columns (HR 0.5, HR 1, HR 3 and HR 4, Waters Styragel columns run in series with column pore sizes of 50, 100, 500 and 1000 Å, respectively). THF with triethylamine (to prevent the adsorption of the hydrophilic polymer on the column) was used as the mobile phase at a flow rate of 1.0 mlpermin. The dn/dc values for the polymers in THF at 40 °C were measured with an LED (Optilab DSP) source. After the dn/dc values were measured for five different concentrations for the PHIC sample, size exclusion chromatography -multi-angle laser light scattering detector system data were obtained using refractive index detection at 40 °C.

Thin film preparation

PHIC solutions (1 wt% polymer) were prepared in chloroform (CHCl3) and then spin-coated onto silicon substrates at 2000, r.p.m. for 40 s, which was followed by drying under vacuum at room temperature for 12 h. The obtained thin films (60–70 nm thick) were then annealed at room temperature under CHCl3, carbon disulfide (CS2), or toluene vapor. The CHCl3-annealing was conducted for 3 h. The CS2 annealing was performed for 1 h, whereas the toluene annealing was conducted for 5 h. After this step, the solvent-annealed films were dried under vacuum at room temperature for 1 day. These solvent-annealing and subsequent drying steps were repeated one or two times for some of the first solvent-annealed films by changing the solvent (CS2 or toluene); for example, some of the 1st CS2-annealed films were subsequently annealed with toluene, whereas some of the first toluene-annealed films were then annealed with CS2.

Synchrotron grazing incidence X-ray scattering (GIXS) measurements

GIXS measurements were performed at beamline 3C19, 20, 21, 22, 23 of the Pohang Accelerator Laboratory at the Pohang University of Science and Technology. The diffraction patterns were recorded at a sample-to-detector distance of 123 mm with an X-ray wavelength of λ=0.138 nm using a two-dimensional (2D) charge-coupled detector (Mar, USA). The samples were mounted on a homemade z axis goniometer equipped with a vacuum. The incidence angle, αi, of the X-ray beam was set at 0.150°, which is between the critical angles of the films and the silicon substrate; with this αi value, the X-ray beam can penetrate into the entire polymer film layer. All of the GIXS measurements were conducted at 25 °C. Each diffraction pattern was collected for 30 s. The measured scattering data were quantitatively analyzed using the GIXS formulas derived for several structural models, including hexagonally close packed cylinders and a multilayer structure (Supplementary Information).

Results and discussion

NMR and IR spectroscopic analyses confirmed that the PHIC polymer was successfully synthesized. The number average molecular weight and polydispersity index of the polymer were determined to be 61 000 and 1.20, respectively.

The structures of the solvent-annealed polymer films were examined using GIXS with a synchrotron radiation source. The scattering pattern of the as-cast PHIC film was complicated and weak in intensity (Figure 1a). A similar scattering pattern was observed for the film that underwent subsequent annealing under CHCl3 vapor (Figure 1b); however, the scattering peaks were enhanced in intensity and sharpened in shape. The scattering pattern exhibited periodic anisotropic rings (marked with L1, L2 and L3 in Figure 1a; Table 1) along the αf direction. The positions of these rings relative to the specular reflection position were 1, 2 and 3, and their scattering angles were 4.84°, 9.67° and 14.52°, respectively. This scattering feature indicated the presence of lamellae stacked along a direction normal to the film plane. The film exhibited three additional arc-like spots at αf=5.93°, 11.89° and 17.38° (marked with H1, H2 and H3, respectively, in Figure 1a; Table 1), which suggests the presence of a poorly developed ordered structure in the film in addition to the lamellar structure described above. However, drawing any firm conclusions about an exact ordered structure from such weak, broad scattering peaks is difficult. Overall, both the as-cast film and the CHCl3-annealed film presented at least two different molecular packing orders with different chain conformations. The degree of ordering and the fraction of the film composed of these structures (namely, a lamellar structure and another ordered structure) were relatively low in both films; the degree of ordering was significantly lower in the as-cast film than in the CHCl3-annealed film, as was the fraction of the film occupied by the structures in question.

Table 1 Scattering peaks and their d-spacings from the 2D-GIXS patterns measured for the as-cast and CHCl3-annealed PHIC films

Surprisingly, the CS2-annealed film demonstrated a very clean, crystal-like scattering pattern (Figure 2a). The pattern clearly exhibited several scattering spots, with regular spacings of <15°. These scattering spots satisfied the Bragg conditions for a hexagonal reciprocal lattice of cylinders lying in the film plane. Some representative scattering spots were assigned (Supplementary Figure S3). The scattering spots at αf=5.93° and 11.87° along the αf direction, at 2θf=0°, were indexed as the reflection peaks of the (01) and (02) planes, respectively. The d-spacing was determined to be 1.34 nm for the first-order spot and 0.67 nm for the second order spot. Two additional scattering spots (one at αf=2.92° and 2θf=5.04° and the other at αf=5.85° and 2θf=9.97°) were assigned as the reflection peaks of the (10) and (20) planes, respectively. The d-spacings of these reflections were determined to be 1.34 and 0.67 nm, respectively. Here, the d-spacing of 1.34 nm corresponded to the mean interdistance between the cylinder layers in the hexagonal structure. The scattering spot at αf=8.90° and 2θf=5.04° was indexed as the reflection peak of the (11) plane, and its d-spacing was determined to be 0.77 nm. From these results, the mean interdistance of the cylinders was estimated to be 1.55 nm. In addition, the scattering pattern contained a weak, broad, isotropic scattering ring at 17.70°. The d-spacing of this ring was estimated to be 0.45 nm. Considering an in-plane oriented hexagonal packing order of PHIC polymer chains, this isotropic scattering ring can only originate from the n-hexyl side groups along the individual polymer chain backbones in a helical conformation. The n-hexyl groups in the nearest neighboring positions might have the highest population, which exhibits a maximum intensity in the isotropic scattering ring. Taking this situation into consideration, the d-spacing (=0.45 nm), which was determined from the peak maximum of the isotropic scattering ring, can be assigned to the mean interdistance of the nearest neighbored n-hexyl groups along the single-PHIC polymer chain in a helical conformation (which is a structural member of the in-plane oriented hexagonal packing order). Considering this fact, we performed calculations on all of the possible helical conformations (21, 51, 85, 125 and so on) for the PHIC polymer chain using the Cerius2 software package (Accelrys, San Diego, CA, USA). The resulting d-spacing value (=0.45 nm) of the isotropic scattering ring at the maximum intensity is very similar to the interdistance of the neighboring n-hexyl side groups in the PHIC chain with the 83 helical conformations, rather than any other conformations. This result is, for the first time, direct experimental evidence for the helical conformation of PHIC chains in a hexagonal packing structure. Furthermore, the results also confirmed that synchrotron GIXS is a very unique, powerful technique for determining polymer chain conformations and their hierarchical structures.

Figure 2
figure 2

2D-GIXS patterns measured at αi=0.150° for PHIC thin films deposited onto silicon substrates: (a) CS2-annealed for 1 h; (b) toluene-annealed for 5 h after CS2-annealing; (c) CS2-annealed for 1 h after CS2- and toluene annealing in sequence. Scattering patterns reconstructed from the determined structural parameters (Tables 2 and 3) using the GIXS formula: (A) HCP structure determined from an analysis of the pattern in (a); (B) multi-bilayer structure determined from an analysis of the pattern in panel (b); (C) HCP structure determined from an analysis of the pattern in panel (c).

With the above information, the 2D-scattering pattern (Figure 2a) was quantitatively analyzed using the GIXS formula for a hexagonal close packing (HCP) structure model (Figure 3a and Supplementary Figure S4), which allowed all of the structural and orientation parameters to be determined. The results from the data analysis are summarized in Table 2. The determined molecular chain conformation and HCP structure are shown in Figure 3a. This analysis confirmed that the CS2-annealed film formed a HCP structure where the molecular PHIC cylinders lie in the film plane. The lattice parameter (dHCP) of the HCP structure was determined to be 1.55 nm, which is the mean interdistance of the molecular PHIC cylinders. The length of the fully extended n-hexyl group was calculated to be 0.83 nm using the Cerius2 software package. Considering this side group length and the 83 conformations, the molecular PHIC cylinder was determined to have a diameter of 1.55 nm. This cylinder diameter is the same as the lattice parameter, dHCP, of the HCP structure, which confirms that the molecular PHIC cylinders were closely packed with each other in the structure. Interestingly, the analysis revealed that the molecular PHIC cylinder consists of a relatively dense core region (whose radius, Rc, is 0.310 nm) and a less dense shell region with a thickness of 0.465 nm (Rs); here, the core region was composed of the polymer backbone and the inner parts of the n-hexyl side groups, whereas the shell region consisted of the remaining parts of the side groups. Furthermore, the results collectively revealed that no interdigitation occurred between the neighboring, contacting molecular cylinders. In addition, the helical molecular cylinders were observed to have very small values for the positional distortion factors (g10=g11=g01=0.057), which indicates that all of the helical molecular PHIC cylinders are stably positioned in the HCP structure. For the HCP structure, the orientational order parameter, Os, was determined (with respect to the normal to the film plane) to be 0.999, thereby confirming that the helical molecular PHIC cylinders of the HCP structure are almost completely lying in the film plane. From the structural model with these parameters, a scattering pattern was reconstructed using the GIXS formula; this pattern matched well with the measured scattering pattern (Figures 2a and A).

Figure 3
figure 3

Molecular conformation and packing order of PHIC in thin films and their reversible transformations via selective solvent-annealing: (a) HCP structure with 83 helical conformation; (b) molecular multi-bilayer structure with β-sheet conformation.

Table 2 Structural parameters of the PHIC films (which were annealed with CS2 or consecutively annealed with CS2, toluene and CS2) determined by GIXS measurements and data analysis

The CS2-annealed films were subsequently annealed under toluene vapor. The toluene-annealed films were examined using GIXS. Surprisingly, these films also exhibited a 2D-scattering pattern, but it was considerably different from the pattern observed for the CS2-annealed films. The scattering pattern was observed to be identical to that of the as-cast films that were annealed with toluene. The films exhibited periodic arc peaks with regular spacing along the αf direction at 2θf=0°; αf=4.84°, 9.67°, and 14.52° (Figure 2b). The appearance of these scattering peaks suggests that a lamellar structure is present in the film and that its lamellae are stacked along a direction normal to the film plane. The d-spacing of the first-order arc peak was determined to be 1.64 nm, which was larger than the diameter of the 83 helical conformational polymer chain but was very close to twice the length (0.83 nm) of the fully extended n-hexyl group. Considering a lamellar structure, the d-spacing value may correspond to the long period (that is, the layer thickness). The scattering pattern exhibited additional arc peaks along the 2θf direction at αf=0°; 2θf=12.07°, 16.32° and 18.53°, which corresponded to d-spacings of 0.66, 0.49 and 0.43 nm, respectively. These peaks may have resulted from the lateral packing of the polymer backbones and the side groups.

Considering these results, the scattering pattern was analyzed in detail using the GIXS formula for a molecular multi-bilayer structure model (Figure 3b and Supplementary Figure S4). The results of the analysis are summarized in Table 3. The determined structural model is shown in Figure 3b. The 2D-scattering pattern reconstructed with the structural model was confirmed to match well with the measured pattern (Figures 2b and B). Collectively, these results indicate that the toluene-annealed film consisted of a well-ordered molecular multi-bilayer structure of the fully extended polymer chains in the 21 conformation with no interdigitation between the side groups of adjacent molecular layers. For the multi-bilayer structure, the orientational order parameter, Os, was determined (with respect to the normal to the film plane) to be 0.963, which indicates that the layers were preferentially stacked in the out-of-plane direction of the film. In this structure, the long period, d3, of the lamellae was determined to be a thickness of 1.67 nm. Furthermore, the individual lamellae were composed of two sublayers, namely a relatively dense sublayer and a less dense sublayer; the dense sublayer (with a thickness of 0.77 nm (=h1)) consisted of the backbone and the inner parts of the side groups, whereas the less dense sublayer (with a thickness of 0.87 nm (=h2)) consisted of the remaining parts of the side groups from the adjacent two polymer chains (Figure 3b). This structural analysis also revealed a mean interdistance of 0.66 nm (=dr1) for the n-hexyl side groups between the neighboring polymer chains, whose repeat units were matched in position along their backbones (see the front and top views in Figure 3b); the mean interdistance of these side groups corresponded to the arc-scattering peak at 2θf=12.07° at αf=0° (Figure 2b). In the multi-bilayer structure, the n-hexyl side groups along the backbone of the PHIC polymer chain were determined to have a lateral mean interdistance of 0.49 nm (=dr2) (see the side and top views in Figure 3b), which corresponded to the arc-scattering peak that appeared at 2θf=16.32° at αf=0° in Figure 2b. The side groups between the nearest neighboring polymer chains were observed to have a mean interdistance of 0.43 nm (=dr3) (see the top view in Figure 3b), which corresponded to the arc-scattering peak at 2θf=18.53° at αf=0° (Figure 2b); here, the repeat units of the nearest neighboring polymer chains were mismatched in position along their backbones. In addition, the n-hexyl side groups were determined to have very small values of positional distortion factors (g33=0.052 and grr=0.048), which reveals that the side groups were stably positioned in the out-of-plane and in-plane directions of the multi-bilayer structure. These results collectively demonstrate that the toluene-annealing process produced a complete phase transformation from a well-ordered HCP structure with 83 helical conformational chains to a well-ordered multi-bilayer structure with 21 helical (that is, β-sheet) conformational chains.

Table 3 Structural parameters of the PHIC films consecutively annealed with CS2 and toluene, which were determined by GIXS measurements and data analysis

When the films were treated again with CS2 vapor, they presented a 2D-GIXS pattern (Figure 2c) similar to that (Figure 2a) observed for the CS2-annealed films before toluene annealing. The scattering peaks were slightly weakened in intensity; furthermore, the isotropic scattering ring at 17.70° became slightly broader and stronger. The scattering pattern was analyzed in detail using a GIXS formula for the HCP structure (Supplementary Figure S4). The obtained structural parameters are listed in Table 2, which are almost identical to those determined for the films annealed with only CS2. From the obtained structural parameters, a scattering pattern was reconstructed using the GIXS formula. The calculated pattern matched well with the measured scattering pattern (Figures 2c and C). These analysis results confirmed that the molecular multi-bilayer structure with β-sheet conformational chains successfully transformed back to an HCP structure with 83 helical conformational chains by the retreatment with CS2 annealing (Figure 3).

The interesting chain conformations and morphological structures described above might result from selective and specific interactions of the PHIC polymer molecule with solvent molecules during the solvent-annealing process. We observed that CHCl3 is a good solvent for PHIC, where CS2 and toluene are relatively less good solvents. PHIC is composed of a relatively polar amide backbone and nonpolar n-hexyl side groups. CHCl3 is a polar solvent. Therefore, the polar CHCl3 molecule has a higher affinity for the amide units in the backbone than for the n-hexyl side groups. The favorable interaction of the solvent molecules with the amide backbone units can cause the rigid polymer backbones to mobilize, and then the mobilized backbones consequently cause their flexible n-hexyl side groups to mobilize. Owing to the good solvent characteristics and the polar nature, the CHCl3 molecule might interact more strongly with the amide backbone units, although the polymer backbone has considerable chain rigidity. As a result, the entire polymer chain is highly mobilized and consequently has less selectivity in its chain conformation and formation of its self-assembled structure, which leads to a mixture of two different conformations (83 and 21) and their own self-assembled structures in mixed phases (that is, a mixture of the hexagonal lattice structure with the 83 chain conformation and the multi-bilayer structure with the 21 chain conformation).

In contrast, toluene is a nonpolar solvent. Therefore, the nonpolar toluene has a higher affinity for the n-hexyl side groups than for the amide backbone. The favorable interaction of the solvent molecules and the n-hexyl side groups can cause the flexible alkyl side groups to mobilize. Then, the mobilized alkyl side groups subsequently try to direct the amide chain backbone to mobilize. However, this mobilization of the amide chain backbone might be limited to a certain degree because the polymer backbone has considerable chain rigidity and the toluene solvent has less good solvent characteristics and is nonpolar. Therefore, the limited mobilization of the polymer backbone may cause negative feedback to the mobility of the n-hexyl side groups. As a result, the overall mobility of the PHIC chain induced by toluene vapor is relatively lower. Specifically, the toluene-induced mobility of the polymer backbone is significantly less than that induced by CHCl3. Under this circumstance, the alkyl side groups appear to form a smectic A-like ordering rather than a well-defined lattice ordering or full disordering. This ordering subsequently induces the polar amide backbones that have a limited mobility to pack closely together via their electron donor and acceptor interactions. These interactions collectively lead the PHIC molecules to form a multi-bilayer structure with a β-sheet chain conformation.

CS2 is also a nonpolar solvent. In fact, in this molecule the sulfur atoms have relatively larger size (that is, volume), higher polarizability, higher electron affinity and higher electronegativity, compared those of the carbon atom.24 Furthermore, the sulfur atoms in the CS2 molecule are known to have weaker π-donor ability, which makes the carbon center atom more electrophilic.25, 26 Therefore, each C=S bond has a dipole moment, even though the magnitude of the dipole moment is low. These two C=S bonds are linearly linked via the carbon center, and therefore, their molecule CS2 has no permanent dipole moment. Although CS2 is a nonpolar solvent, it presents locally weak polarity on each building element. Because of these characteristics, CS2 has a different chemical nature than toluene. Furthermore, these characteristics are known to make CS2 more reactive than carbon dioxide (CO2).26, 27, 28, 29, 30 Owing to the overall nonpolar characteristic, the CS2 molecule might have a favorable level of affinity for the n-hexyl side groups. Because of the local polarities, the CS2 molecule might also have a favorable level of affinity for the amide backbone. The observed less good solvent characteristics suggest that the interactions of the alkyl side groups and the amide backbone with CS2 occur to a marginal degree. The interaction of the alkyl side groups with CS2 might be less than their interaction with toluene; however, the interaction of the amide backbone with CS2 might be greater than with toluene but considerably less than with CHCl3. Overall, the CS2 solvent molecule primarily induces both the rigid amide backbone and the n-hexyl side groups to mobilize in a proper level via favorable interactions in marginal levels; note that the mobility of the polymer backbone induced by CS2 appears to be greater than that induced in a secondary process by the nonpolar toluene but considerably less than that induced by the polar CHCl3. Such cooperative interactions collectively lead the PHIC molecules to have the 83 helical conformations and form the HCP structure.

As discussed above, the chain conformation and formation of a self-assembled structure of the peptide-mimic rigid PHIC was well controlled by annealing under vapors of an appropriate solvent that can properly interact with the polymer chain. During the solvent-annealing process, it is very important to manage the specific interactions of a chosen solvent molecule with the polymer building components and their level in the appropriate way to provide the overall and local mobilities of the polymer chain required to form a certain chain conformation and its self-assembled structure.


For the first time, we succeeded in producing well-ordered PHIC structures with the aid of selective solvent-annealing, and we determined the details of their structures and conformations. PHIC formed a well-ordered HCP structure with 83 helical conformational chains in the film that was annealed under vapors of CS2 (a less good solvent), which is a nonpolar solvent but has locally weak polarity on its building elements, and a well-ordered multi-bilayer structure with 21 (β-sheet) conformational chains in the film annealed under vapors of toluene, which is a nonpolar solvent and also another type of less good solvent. A fully reversible transformation between these two structures was observed by consecutive annealings with CS2 and toluene.


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This study was supported by the National Research Foundation of Korea (Doyak project (2011-0028678) and the Center for Electro-Photo Behaviors in Advanced Molecular Systems (2010-0001784)), the Program for Integrated Molecular System of GIST and the Ministry of Education, Science and Technology (MEST) (BK21 Program and World Class University Program R31-2008-000-10059-0 and R31-20008-000-10026-0). The synchrotron X-ray scattering measurements at the Pohang Accelerator Laboratory were supported by MEST and POSCO Company, and POSTECH Foundation.

Author contributions

M.R. and J.-S.L. designed the research and initiated the study. J.M. and P.N.S. synthesized and characterized the material. Y.R., B.A., S.J., and K.K. conducted sample preparations and GIXS measurements. Y.R. and J.Y. did set up the theoretical GIXS framework and performed the data analyses. M.R., J.-S.L., Y.R., J.M., and J.Y. prepared the manuscript. All authors contributed to the discussion.

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Correspondence to Jae-Suk Lee or Moonhor Ree.

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The authors declare no conflict of interest.

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Supplementary Information accompanies the paper on the NPG Asia Materials website

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Rho, Y., Min, J., Yoon, J. et al. Reversible conformation-driven order–order transition of peptide-mimic poly(n-alkyl isocyanate) in thin films via selective solvent-annealing. NPG Asia Mater 4, e29 (2012).

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  • conformation change
  • hexagonal close packing structure
  • multi-bilayer structure
  • peptide-mimic poly(n-alkyl isocyanate)
  • reversible order–order transition
  • selective solvent annealing
  • self-assembly

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