A series of poly(ethylene oxide)-b-polystyrene (PEO-b-PS) diblock copolymers were designed
and synthesized to study the change in crystal orientation of PEO blocks under different confinement
sizes. The volume fraction of PEO blocks (f
PEO) in these copolymers was kept almost identical (the f
PEO
values were between 0.45 and 0.48) but with different number-average molecular weights for the PS and
PEO blocks (M̄
n
PEO and M̄
n
PS). Therefore, the phase morphology of these copolymers was a lamellar
structure with different PEO and PS layer thicknesses (d
PEO and d
PS) detected by synchrotron small-angle X-ray scattering (SAXS) experiments. Since the melting temperature of these PEO crystals is lower
than the glass transition temperature of the PS layers, the PEO block crystals could be melted and
recrystallized under one-dimensional (1D) confinement at different crystallization temperatures (T
c). The
PEO block crystal orientation changes were monitored using synchrotron wide-angle X-ray diffraction
(WAXD) experiments. It was found that the crystalline PEO chain orientation (the c-axis in the crystals)
underwent a change from being perpendicular (homogeneous) to the layer normal direction (n̂) at low
T
cs to parallel (homeotropic) at high T
cs in these 1D confined samples with the d
PEO ranging from 8.8 to
23.3 nm. However, with the gradual release of this 1D confinement, i.e., increasing the d
PEO, a broad T
c
region in which the inclined c-axis orientation was originally observed in the PEO-b-PS with the low
M̄
n
PEO (8.7K g/mol) and M̄
n
PS (9.2K g/mol) became increasingly narrowed by pushing the starting T
c where
the tilting initiates toward higher T
c and reducing the ending T
c where the parallel orientation of the
c-axis with n̂ starts. In the PEO-b-PS sample with the highest M̄
n
PEO (57K g/mol) and M̄
n
PS (61.3K g/mol)
in this study, this T
c region was narrowed to less than 5 °C, suggesting the confinement size effect on the
crystal orientation of the PEO crystals. The homogeneous to homeotropic orientation change of the c-axis
in the PEO crystals with increasing T
c was explained to be largely governed by the primary nucleation
and crystal growth processes of the PEO blocks for developing the maximum crystallinity. A semiquantitative calculation was attempted to illustrate why the homogeneous orientation of the PEO crystals
takes place in the 1D confinement based on the SAXS, WAXD, and differential scanning calorimetric
results. It was expected that when the d
PEO becomes large enough, the homogeneous orientation of the
c-axis in the PEO crystals would disappear.