Contrary to most or all other materials, crystallization of chiral but race
mic polymers such as isotactic polypropylene is accompanied by a conformati
onal rearrangement which leads to helical geometries: the building units of
the crystal are helical stems, approximate to 10-20 nm long, which can be
either right-handed or left-handed. Helical hand cannot be reversed within
the crystal structure: it is therefore a permanent marker and an indicator
of molecular processes tin particular segregation/selection of helical hand
s) which take place during crystal growth, and more precisely during the cr
ucial step of "efficient" helical stem deposition. The issue of proper heli
cal hand selection during polymer crystal growth is mainly illustrated with
isotactic polypropylene. Its various crystalline polymorphs (alpha, beta,
gamma and smectic) display virtually all possible combinations of helical h
ands, azimuthal settings and even non-parallel orientation of helix axes in
space. Furthermore, a specific homoepitaxy which generates a lamellar bran
ching in the ct phase "quadrites" and alpha/gamma composite structures make
s it possible a) to determine the helical hand and associated azimuthal set
ting of every stem in the crystalline entities and b) to determine the impa
ct on the crystal structure and morphology of "mistakes" in helical hand of
the depositing stem. Analysis of these morphologies demonstrates that the
crystallization of isotactic polypropylene land by implication of other ach
iral, helical polymers) is a highly sequential and "substrate-determined" p
rocess, i.e. that. the depositing stem probes the topography of the growth
face prior to attachment. These observations appear difficult to reconcile
with crystallization schemes in which molecules (helical segments) are prea
rranged in a kind of pseudo-crystalline bundle land as such, are not subjec
ted to the high constraints of crystal symmetry) before deposition as a pre
assembled entity on the substrate.