142 Advances in Polymer Science Editorial Board: A. Abe. A.-C ...
142 Advances in Polymer Science Editorial Board: A. Abe. A.-C ...
142 Advances in Polymer Science Editorial Board: A. Abe. A.-C ...
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Asymmetric Star <strong>Polymer</strong>s Synthesis and Properties 121<br />
overall degree of polymerization, of sample SI 2 near the ODT were higher than<br />
<strong>in</strong> the case of diblocks of the same composition and almost <strong>in</strong>dependent of temperature.<br />
The broad distribution of relaxation times (longer than the relaxation<br />
times of <strong>in</strong>dividual cha<strong>in</strong>s) observed by rheology was attributed to a broad distribution<br />
of gra<strong>in</strong> sizes. At very long times the rheological behavior of the samples<br />
was proposed to be governed by the relaxation of gra<strong>in</strong>s which rearrange<br />
with rates related to their sizes. Quench<strong>in</strong>g experiments were used to elucidate<br />
the mechanism govern<strong>in</strong>g the order<strong>in</strong>g process. The rheological measurements<br />
after each quench from the melt <strong>in</strong>dicated that order<strong>in</strong>g proceeds via heterogeneous<br />
nucleation. Quench<strong>in</strong>g to f<strong>in</strong>al temperatures near the ODT made the k<strong>in</strong>etics<br />
very slow with times which depended strongly on the f<strong>in</strong>al quench temperature.<br />
Deeper quenches produced only moderate changes <strong>in</strong> the k<strong>in</strong>etics.<br />
Compared with diblocks the k<strong>in</strong>etic times were slower for miktoarm stars <strong>in</strong><br />
deeper quenches. For shallow quench<strong>in</strong>g there were no measurable differences.<br />
The width of the k<strong>in</strong>etically accessible metastable region was also larger for the<br />
star copolymers. External perturbations, i.e., cont<strong>in</strong>uous oscillat<strong>in</strong>g shear, produced<br />
no changes <strong>in</strong> the order<strong>in</strong>g process.<br />
Dielectric spectroscopy was also used by the same group <strong>in</strong> order to study the<br />
local and global dynamics of the PI arm of the same miktoarm star samples [89].<br />
Measurements were conf<strong>in</strong>ed to the ordered state, where the dynamics of the PI<br />
cha<strong>in</strong> tethered on PS cyl<strong>in</strong>ders were observed <strong>in</strong> different environments s<strong>in</strong>ce <strong>in</strong><br />
the SIB case the faster mov<strong>in</strong>g PB cha<strong>in</strong>s are tethered <strong>in</strong> the same po<strong>in</strong>t as the PI<br />
arm. The distribution of segmental relaxation times were broader for SI 2 than<br />
SIB. The effect was less pronounced at higher temperatures. The PI normal<br />
mode time was found to be slower <strong>in</strong> SIB, when compared to SI 2 although both<br />
arms had the same molecular weight. Additionally, the normal mode relaxation<br />
time distributions of the PI cha<strong>in</strong>s tethered to PS cyl<strong>in</strong>ders <strong>in</strong> the miktoarm<br />
samples were narrower than <strong>in</strong> P(S-b-I) systems of lamellar structure.<br />
The characteristics of the order-disorder transition <strong>in</strong> two SI 3 miktoarm stars<br />
were also <strong>in</strong>vestigated by Floudas et al. us<strong>in</strong>g SAXS and rheology [78]. Due to the<br />
high molecular weights diisooctylphthalate (DOP) was used as the nonpreferential<br />
solvent to br<strong>in</strong>g the transition <strong>in</strong>to the experimentally accessible temperature<br />
w<strong>in</strong>dow. All SAXS parameters were discont<strong>in</strong>uous at the ODT reveal<strong>in</strong>g a<br />
first-order transition. The <strong>in</strong>teraction parameter exhibited a weak temperature<br />
dependence consistent with fluctuation effects near the transition. The experimental<br />
results agreed qualitatively with the theoretical sp<strong>in</strong>odal curves cN total =<br />
F(f A) for AB n miktoarm copolymers. For shallow quenches rheological measurements<br />
<strong>in</strong>dicated a nucleation and growth order<strong>in</strong>g mechanism with an Avrami<br />
exponent of about three, rem<strong>in</strong>iscent of undiluted block copolymers.<br />
Floudas and coworkers [90] employed dielectric spectroscopy to probe the <strong>in</strong>terfacial<br />
width <strong>in</strong> lamellae form<strong>in</strong>g non-l<strong>in</strong>ear block copolymers of the type (Bb-A)<br />
3B and (B-b-A) 3B(A-b-B) 3, where A is PI and B is PS. Their experiments<br />
were conducted at temperatures below the ODT and below the glass transition<br />
of the PS “hard phase”. In this temperature region the global cha<strong>in</strong> dynamics of<br />
PI bridges were used to provide an estimate of the “dynamic” <strong>in</strong>terface between