Poster Session, Thursday, June 17Theme F686 - N1123A Rheological Model For Determ<strong>in</strong><strong>in</strong>g Degree Of Exfoliation In Polymer/Clay Nanocomposites1 Hosse<strong>in</strong> Ebrahimiand Ahmad Ramazani S. 21 Islamic Azad University ( South Tehran Branch), Tehran,Iran2 Department of Chemical and Petroleum Eng<strong>in</strong>eer<strong>in</strong>g, Sharif University of Technology,Tehran,IranAbstract— We present a conformational based model for prediction rheological behavior of nanocomposite. The EVA/clayand EVA/PE/clay nanocomposites with different nanoclay contents were prepared by melt mix<strong>in</strong>g. The model calculations forthe start-up viscosity are compared with experimental result. Then, a relation for determ<strong>in</strong><strong>in</strong>g degree of exfoliation ofnanoparticles <strong>in</strong> polymeric matrix was derived.The degree of exfoliation, <strong>in</strong>tercalation and dispersion ofpolymer/clay nanocomposites traditionally characterized byX-ray diffraction (XRD) and transmission electronmicroscopy(TEM); while both are effective tools, they are stilllimited <strong>in</strong> that they only probe a small volume of the sampleand can be costly for rout<strong>in</strong>e characterization ofnanocomposites. Further, XRD nor TEM alone cannotaccuracy describe the level of clay dispersion and polymernanocomposite structure. Rheologyical <strong>in</strong>vestigation givesimportant <strong>in</strong>formation about the structure formation dur<strong>in</strong>g thesynthesis of polymer/clay nanocomposites.In this study, a conformational based model for predictionrheological behavior of nanocomposite was presented. Theconformational rheological models relate the stress tensor tothe molecular conformation change concept dur<strong>in</strong>g andso it seems that these models can be extendedphenomenologically for a system, which <strong>in</strong>cludes polymer andparticles. In this model two micro structural state variablecalled conformation tensor c and orientation tensor show thestate of deformation of polymer molecules and orientation ofparticles dur<strong>in</strong>g flow, respectively.For a non-compressible polymer fluid with amicrostructure represented by a second order symmetrictensor, c, the Poisson bracket formalism leads to the follow<strong>in</strong>gequations for the time evolution of c [1, 2 and 3]:c1 . . 1 ( . cc. ) ( cc. ) :t2 2c2( c. )cIn wich is a fourth-order tensor, called the mobilitytensor, is the rate of stra<strong>in</strong> tensor, is the vorticity tensor , stress tensor, and is the Helmholtz free energy.To derive the time evolution equations for orientation tensor , nanoparticles will be modeled <strong>in</strong>side the framework of thetime evolution equation for the fiber orientation tensor byFolgar and Tucker, 1984; Advani and Tucker 1987[4]:d a , 1 1 . . . . ( a a. . a a. 2 : aa) 2cI ( 0a)dt2 , 2 , ,.<strong>in</strong> wich and are respectively the rate-of-stra<strong>in</strong> tensor andthe vorticity tensor. is related to the aspect ratio of the fibers.( =[(l/d) 2 - 1]/[(l/d) 2 +1], l and d represent respectively thefiber length and diameter, 0 is a constant equal to 3 for a 3Dorientation and 2 for a 2D orientation <strong>in</strong>troduced <strong>in</strong> order tosatisfy the constra<strong>in</strong>t tr a = 1. C I is the <strong>in</strong>teraction coefficientparameter. With some modification <strong>in</strong> the above equations,we derive a new class of equations that can analyze the effectsof different parameters to model. This model developed for<strong>in</strong>tercalate and exfoliated systems.To prove the model, the EVA/clay and EVA/PE/claynanocomposites with different nanoclay contents wereprepared by melt mix<strong>in</strong>g. The model calculations for the startupviscosity are reasonably <strong>in</strong> agreement with theexperimental results both <strong>in</strong> exfoliated and <strong>in</strong>tercalatedsystems. Compar<strong>in</strong>g experimental results and modelcalculation was derived a relation that determ<strong>in</strong>eapproximately degree of exfoliation of system.*Correspond<strong>in</strong>g author: ebrahimi_h@yahoo.com[1] H. Eslami, A. Ramazani S. A., H. A. Khonakdar, Macromol. TheorySimul. 12, 524-530(2004).[2] A. Ramazani, M.Grmela, A. Kadi, J. Rheol. 3, 51(1999).[3] A. Ramazani, A. Ait-Kadi, M. Grmela, J. Non-Newtonian Fluid Mech. 73,241(1997).[4] J.S. C<strong>in</strong>tra, Jr and C.L. Tuker III, J. Rheol. 39(6), 1095, (1995).[5] R. Guenette and M. Grmela, J. Non-Newtonian Fluid Mech. 45,187(1992).[6] M. Grmela, P. J. Carreau, J. Non-Newtonian Fluid Mech. 23, 271(1987).[7] A.N.Beris,B.J.Edwards, Thermodynamics of flow<strong>in</strong>g systems, 1 st edition,OxfordUniversityPress,NewYork(1994).[8] R.B. Bird, R.C. Armstrong and O. Hassager, Dynamics of PolymericLiquids: vol. 1, Fluid Mechanics, 2 st edition, Wiley-VCH, New York (1987).[9] A. Ramazani, A. Ait-Kadi, M. Grmela, J. Non-Newtonian Fluid Mech.73,241(1997).[10] M. Rajabian, C. Dubois, M. Grmela and P.J. Carreau, Rheol. Acta 47,701 (2008).6th Nanoscience and Nanotechnology Conference, zmir, 2010 723
P onPP toP coord<strong>in</strong>atedPPoster Session, Thursday, June 17Theme F686 - N1123The Study of Effect of Au(III) ion on the Thermal Degradation of Different Copolymers via DirectPyrolysis Mass Spectrometry111UCeyhan Kayran UP P, Tugba OrhanP Pand Jale HacalogluP P*1PDepartment of Chemistry, Middle East Technical University, 06531 Ankara, TurkeyAbstract- In this work, thermal degradation of different copolymers namely, polystyrene-block-poly(2v<strong>in</strong>yl pyrid<strong>in</strong>e) (PS-b-P2VP),polyisoprene-block- poly(2v<strong>in</strong>yl pyrid<strong>in</strong>e) (PI-b-P2VP) and poly(2v<strong>in</strong>yl pyrid<strong>in</strong>e)-block-polymethylmetacrylate (P2VP-b-PMMA) and the effect3+of coord<strong>in</strong>ation of AuP thermal degradation mechanisms were studied via direct pyrolysis mass spectrometry. The metal functionalcopolymers were also characterized by classical techniques such as TEM, ATR-FT-IR and UV-vis spectrometry.Today’s material science deals <strong>in</strong>creas<strong>in</strong>gly withnanostructures, i.e., with structures of characteristicdimension between 1 and 100 nm [1]. For build<strong>in</strong>g upsmaller structures, nature may serve as a model, where byself-organization and build<strong>in</strong>g up compartments, <strong>in</strong>dividualmolecules are <strong>in</strong>tegrated <strong>in</strong>to larger functional units andstructural hierarchies. One s<strong>in</strong>gle self-organization step isoften not sufficient to realize functional systems. Thesynthesis of metal clusters <strong>in</strong> micro compartments of selforganizedpolymer systems offers the advantage to restrictthe size growth of the particles to a predef<strong>in</strong>ed diameter andto prevent the particles from further aggregation. If the microcompartments are arranged on a superlattice, this k<strong>in</strong>d ofsynthesis leads the nanoparticles to become also <strong>in</strong>tegrated<strong>in</strong>to the lattice. This gives rise to the formation ofnanostructured <strong>in</strong>organic/polymer hybrid materials. Theextremely large <strong>in</strong>organic/polymer <strong>in</strong>terface can bestabilized by attach<strong>in</strong>g appropriate ligands to the polymerblocks [2, 3]. Weakly coord<strong>in</strong>ated metal complexes serve asprecursor materials which, by complex formation with theligands, can be solubilized <strong>in</strong>to the polymer compartments.There should not be too strong complexation between theprecursor and the ligand, as otherwise, there will be nofurther reaction to the elementary metal.Recently, methods of synthesiz<strong>in</strong>g nanoclusters <strong>in</strong> microphaseseparated diblock copolymers hav<strong>in</strong>gpolyv<strong>in</strong>ylpyrid<strong>in</strong>e blocks have been reported that providegreater control over cluster formation [4, 5].In this work, synthesis and characterization ofnanostructural metal ion composites and the effect of3+coord<strong>in</strong>ation of Au PPon thermal degradation of differentcopolymers hav<strong>in</strong>g 2v<strong>in</strong>ylpyrid<strong>in</strong>e unit, (polystyrene-bpoly(2v<strong>in</strong>ylpyrid<strong>in</strong>e)(PS-b-P2VP), polyisoprene-bpoly(2v<strong>in</strong>ylpyrid<strong>in</strong>e) (PI-b-P2VP) and poly(2v<strong>in</strong>ylpyrid<strong>in</strong>e)-b-polymethylmetacrylate (P2VP-b-PMMA)) were studied.The samples were characterized via classical techniques suchas TEM, ATR-FT-IR, UV-vis spectrometry. TEM imagesproved the formation of nanoparticles. The disappearance ofcharacteristic peaks due to pyrid<strong>in</strong>e stretch<strong>in</strong>g and bend<strong>in</strong>gmodes <strong>in</strong> the FTIR spectra of the samples confirmed thecoord<strong>in</strong>ation of metal ions to the pyrid<strong>in</strong>e nitrogen.Furthermore, the peak due to CO stretch<strong>in</strong>g of PMMAdecreased <strong>in</strong> <strong>in</strong>tensity while a new absorption peak appeared,which revealed that electron deficient gold (III) ion preferscoord<strong>in</strong>ation from both donor atoms of PMMA (namelycarbonyl oxygen and pyrid<strong>in</strong>e nitrogen) <strong>in</strong> order tocompensate its electron deficiency.In the UV-Vis spectra of metal functional copolymers,namely, Au-PS-b-P2VP, Au-P2VP-b-PMMA, Au-PI-b-P2VP the sharp absorption peak at around 290-320 nm wasattributed to a LMCT transition from v<strong>in</strong>ylpyrid<strong>in</strong>e nitrogen3+to AuPPion s<strong>in</strong>ce electron deficient Au(III) ion was ready toaccept electron from pyrid<strong>in</strong>e nitrogen. The pyrolysis mass3+spectrometry analysis showed that coord<strong>in</strong>ation of AuPPtopyrid<strong>in</strong>e nitrogen of poly(2-v<strong>in</strong>ylpyrid<strong>in</strong>e) unit ofcopolymers affected thermal behavior almost similarly. Inthe case of P2VP-b-PMMA, besides the coord<strong>in</strong>ation of3+3+AuP P2VP unit, coord<strong>in</strong>ation of electron deficient AuPto carbonyl group of PMMA results a drastic change <strong>in</strong> thethermal stability of PMMA based products as shown <strong>in</strong>Figure 2.41---------------569---------------3Figure 1. Thermal degradation mechanism of MMA monomer.20.00 40.00 60.0020.00 40.00 60.0020.00 40.00 60.00Figure 2. Evolution profiles of MMA monomer dur<strong>in</strong>g the3+pyrolysis of P2VP-b-PMMA, and AuPP2VP-b-PMMAThis work was partially supported by TUBITAK underGrant No. TBAG-106T656.*Correspond<strong>in</strong>g author: ckayran@metu.edu.tr[1] S. Förster, M. Konrad, , J. Mater. Chem., 13, 2671 2003).[2]J.F., Ciebien, R.T., Clay, B.H.,Sohn, R.E., Cohen, New J.Chem., 685-691(1998)[3]A., Haryono, W.F., B<strong>in</strong>der, Small, 2, 600-611(2006)[4]T., Hashimoto, M., Harada, N., Sakamoto, Macromolecules, 32,6867-6870(1999)[5]E. T. Tadd, et al., Mat. Res. Soc. Symo. Proc., 703, 33-42(2002)10069416th Nanoscience and Nanotechnology Conference, zmir, 2010 724
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