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P<br />
P<br />
P<br />
P<br />
P<br />
power<br />
P<br />
copolymers<br />
P<br />
and<br />
copolymers<br />
micelles<br />
DPT<br />
P<br />
P<br />
The Influence of the Macromolecular Architecture on the Micellization in Block<br />
*<br />
Copolymer / Homopolymer BlendsTPD<br />
1,2*<br />
1<br />
UE. PavlopoulouUP<br />
P, K. ChrissopoulouP P, S. H. AnastasiadisP<br />
4<br />
5<br />
5<br />
G. PortaleP P, H. IatrouP P, S. PispasP N. HadjichristidisP<br />
1<br />
PFoundation for Research and Technology – Hellas, I.E.S.L., Heraklion, Crete, Greece<br />
2<br />
PUniversity of Crete, Dept. of Materials Science and Technology, Heraklion, Crete, Greece<br />
3<br />
PAristotle University of Thessaloniki, Dept. of Chemical Engineering, Thessaloniki, Greece<br />
4<br />
PESRF, DUBBLE beamline, Grenoble Cedex, France<br />
5<br />
PUniversity of Athens, Dept. of Chemistry, Zografou, Athens, Greece<br />
*epavl@iesl.forth.gr<br />
Micellization of block copolymers in a selective solvent or in a homopolymer matrix has attracted the attention of the<br />
scientific community in the recent years [1]. The increasing interest in such systems arises from the influence of the<br />
micellization and of the micellar characteristics on phenomena like the modification of interfacial activity, controlled drug<br />
delivery, formation of metal nanoparticles and others. Micelles are stable aggregates formed by the self-assembly of the<br />
copolymers whereas micellization often occurs via a procedure which leads to a dynamic equilibrium between micelles, with<br />
a narrow mass and size distribution, and dispersed copolymer molecules. The majority of the studies on block copolymer<br />
micelle, however, concern micellization either in a selective solvent and/or micelles formed by linear diblocks [2,3].<br />
Herein we investigate the effect of macromolecular architecture on micellar formation and micelle characteristics<br />
of block copolymers in homopolymer matrices. A series of (polyisoprene)B2B(polystyrene), IB2BS, graft copolymers with constant<br />
total molecular weight and varying composition, fBPSB, and a series of symmetric (polyisoprene)BnB(polystyrene)BnB, IBnBSBnB,<br />
miktoarm star block copolymers, with n identical pairs of arms, are added to a low molecular weight polyisoprene<br />
homopolymer matrix and the blends are investigated by small-angle X-ray scattering (SAXS) and dynamic light scattering as<br />
a function of copolymer concentration and fBPSB or n, respectively. SAXS measurements have been carried out at the<br />
Daresbury Synchrotron Radiation Source (SRS), UK, and at the Dutch-Belgian Beamline (DUBBLE) at the European<br />
-<br />
Synchrotron Radiation Facility (ESRF) in Grenoble, France, covering a very wide scattering vector range 0.04 < q < 3.7 nmP<br />
1<br />
P. The scattered intensity was corrected for background and transmission whereas measurement of a standard sample<br />
(Lupolen) was utilized for intensity normalization. Analysis of the SAXS scattered intensity [4] allows the measurement of<br />
the form factor of the micelles and, thus, the polystyrene core radius, RBcB, the micellar aggregation number, QBmB, and the<br />
micelle number density, N, can be calculated.<br />
At 2wt% concentration of the IBnBSBnB (with 19k polystyrene and 15k polyisoprene blocks), spherical<br />
micelles are obtained (Figure 1) with a micellar core radius that is independent of n whereas the aggregation number<br />
-1<br />
decreases with n following an nP law (Figure 2). The number density of micelles in the mixture and the polystyrene<br />
fraction in the core are constant as well. These findings signify that, in the range of molecular weights investigated, the<br />
functionality of the junction point of the copolymer does not influence the micellar characteristics. A simple thermodynamic<br />
model has been developed that describes theoretically the micellization of ABnBBBnB within a B homopolymer<br />
matrix. The model agrees very well with the experimental data both qualitatively and quantitatively [5], see Figure 2.<br />
1,3<br />
5<br />
Intensity (cm -1 )<br />
10 -4<br />
10 0<br />
10 0 ESRF<br />
SRS<br />
10 -2<br />
10 -2<br />
10 -4<br />
10 0<br />
10 -2<br />
10 -4<br />
10 0<br />
10 -2<br />
10 -4<br />
10 0<br />
10 -2<br />
10 -4<br />
0.1 1<br />
q (nm -1 )<br />
IS<br />
25<br />
20<br />
15<br />
Experimental<br />
Theoretical<br />
I 2<br />
S 2<br />
10<br />
5<br />
I 4<br />
S 4<br />
0<br />
0 2 4 6 8 10 12 14 16 18<br />
Experimental<br />
250<br />
n<br />
Theoretical<br />
100<br />
200<br />
-1<br />
150<br />
10<br />
1 10<br />
I 6<br />
S 6<br />
I 16<br />
S 16<br />
Q m<br />
R c<br />
(nm)<br />
100<br />
50<br />
Q m<br />
0<br />
0 2 4 6 8 10 12 14 16 18<br />
n<br />
n<br />
Figure 1: The SAXS intensity curves as a function of the<br />
scattering vector q for the 2wt% blends of the various IBnBSBnB<br />
miktoarm copolymers in PI. The curves obtained at ESRF<br />
are presented shifted by an order of magnitude for clarity.<br />
Figure 2: The core radius (RBcB) and the aggregation number<br />
(QBmB) for the IBnBSBnB versus the number of arms n. The<br />
triangles correspond to the theoretical values whereas the<br />
solid circles to the experimental ones with the error bars<br />
determined by the polydispersity in the radii.<br />
145