Die Autoren bedanken sich bei James A. Forrest um Hilfe bei der Idee für diese Technik zu bestätigen. 26. Diese Arbeit wurde durch Mittel aus der University of Pennsylvania unterstützt und wurde teilweise durch die MRSEC Programm der National Science Foundation unter award unterstützt keine. DMR-11- 20901 an der Universität von Pennsylvania.

1. Film: Herstellung <ol><li> Man wiegt 0,04 g Polystyrol, und in einen 30 ml-Fläschchen. </li><li> Wiegen Sie 2 g Toluol in die Flasche. Eine 2% ige Lösung von Polystyrol in Toluol ergibt ein Film von etwa 100 nm. </li><li> Lassen Sie die Lösung sit O / N, um das Polystyrol vollständig zu lösen und lassen Sie die Lösungen zu begleichen. </li><li> Legen Sie eine 1 cm x 1 cm Silizium (Si) Wafer auf einen Spin Coater. </li><li> Drehen Sie das Wafer bei 8000 Upm für 45 sec. Während sie sich dreht, fallen ca. 1 ml Toluol auf dem drehenden Wafers. Hinweis: Alle Schritte, die Schleuderbeschichtung sind in einem Abzug durchgeführt. </li><li> Auf dem nun ortsfesten Si-Wafer, Zugeben der Lösung aus Schritt 1.3 tropfenweise auf den Si-Wafer, bis die gesamte Oberfläche des Si-Wafers bedeckt. </li><li> Bevor die Lösung trocknet auf dem Wafer, drehen Sie das Si-Wafer bei 4.000 Umdrehungen pro Minute für 20 Sekunden. </li><li> Bestimmen Sie die Dicke des Films mit Ellipsometrie (siehe Schritt 2). </li><li> Wenn der Film mit der gewünschten Dicke, anneal den Film in einem Vakuumofen bei 393 K für 15 Stunden. </li></ol> 2. Festlegung der Schichtdicke <ol><li> Legen Sie die Schleudergußfilm auf das Ellipsometer Bühne und messen die ellipsometrischen Winkel Ψ (λ) und Δ (λ) bei einem Lichteinfallswinkel von 70 ° mit einer 1 s Aufnahmezeit und der Zonenmitteleinstellung eingeschaltet. </li><li> Verwendung des Ellipsometers Software passen die resultierende Ψ (λ) und Δ (λ) Daten zu einem Dreischichtenmodell nach dem Protokoll des Herstellers. Es gibt keine zusätzlichen Benutzereingaben. Die erste Schicht ist eine Trägerschicht aus Si, ist die zweite Schicht eine native Oxidschicht mit einer Dicke von 1,5 nm, und die dritte Schicht eine Cauchy-Modell (n = A + B / λ 2, k = 0) ist, entspricht zu den optischen Eigenschaften der Polystyrolfilm. In diesem Modell, A und B die Anpassungsparameter, und n und k die realen und imaginären Komponenten des Index der Refraktion sind. </li><li> Für die Cauchy-Schicht, passen die thickness und A und B Parameter, wenn die Folie mehr als 10 nm ist. Wenn der Film unter 10 nm, nur passen A. Hinweis: Dies wird in der Repräsentative Ergebnisse Abschnitt besprochen werden. </li></ol> 3. Kühlrate Dependent T g Maße <ol><li> Bestreichen Sie die Oberfläche des Heizelements der variable Temperatur Ellipsometer Bühne mit Wärmeleitpaste. </li><li> Platzieren des geglühten Polystyrolfilm auf das Heizelement. </li><li> Klemmen Sie die Folie fest auf das Heizelement. </li><li> Fließen 100% trockene Stickstoffgas durch die Temperaturstufe bei einem Druck von &lt;69 kPa. </li><li> Unter Verwendung der Temperaturstufe-Software, erstellen Sie ein Temperaturprofil. Dieses Temperaturprofil beginnt mit einer Heizrampe bis 393 K auf 150 K / min. Halten Sie den Film bei 393K für 20 min. <ol><li> Dann alternativen Kühlrampen auf 293 K bei Raten von 150, 120, 90, 60, 30, 10, 7, 3 und 1 K / min mit Heizung Rampen auf 393 K bei 150 K / min. Legen Sie ein 5 min Tempetur hold nach jeder Rampe. </li></ol></li><li> In der Ellipsometer-Software sucht, ein temperaturabhängiger Ellipsometrie Modell ähnlich dem in Abschnitt 2. Alle drei Schichten die gleichen sind, außer dass das Substrat auf eine Temperatur abhängigen Si Modell geändert. </li><li> In der Schicht für die temperaturabhängige Si-Modell, schalten Sie die &quot;Use Ext Temp von Parm Log&quot; Parameter. </li><li> Mit Laborgeräten Controlling-Software, haben das Ellipsometer-Software lesen Sie die Temperaturwerte von Temperaturstufe. </li><li> Richten Sie das Ellipsometer, daß das Signal maximaler Intensität erreicht. </li><li> Unter &quot;Hardware Konfigurationen bearbeiten&quot;, stellen Sie die schnelle Erfassungszeit auf 1 Sekunde mit hoher Genauigkeit Zone Mittelwertbildung. Stellen Sie den normalen Aufnahmezeit auf 3 Sekunden mit hoher Genauigkeit Zone Mittelwertbildung. </li><li> Unter der &quot;in situ&quot; Registerkarte im Ellipsometer Software überprüfen Sie die &quot;schnelle Erfassungszeit-Modus&quot; ein, und drücken Sie &quot;Start Acquisition&quot;. Dann startendas Temperaturprofil. Vor der 3 K / min Kühlrampe, deaktivieren Sie das schnelle Erfassungszeit ein. </li></ol> 4. Bestimmung Werte von T g <ol><li> Exportieren Sie die Temperatur und Dickenprofile in den bevorzugten Grafik-und Analyse-Software, und trennen Sie die Temperatur und Dickendaten für alle 9 Kühlraten. </li><li> Um den Effekt der Zone mit durchschnittlich während der Erfassung der Temperatur zu berücksichtigen, nehmen jeden Temperaturwert, und die Durchschnitts es mit dem Temperaturwert vorangeht, so dass T = (T i + T i-1) / 2, wobei T i ist ein Temperaturwert zu einem bestimmten Zeitpunkt und T i-1 ist die Temperatur der vorherigen Zeitpunkt. </li><li> Plot Dicke und Temperatur für jede Kühlrate. </li><li> Durchführen einer linearen Anpassung auf einem Abschnitt des unterkühlten Flüssigregime (Hochtemperaturbereich mit dem größeren Ausdehnungskoeffizienten). Dieses Regime wird ungefähr von 393 K bis 380 K. sein </li><li> Perform lineare Anpassung auf einem Teil der glasartigen Regime des gleichen Satz von Daten. Dieses Regime hat einen niedrigeren Ausdehnungskoeffizienten und wird ungefähr von 293 K bis 340 K. sein </li><li> Finden Sie den Schnittpunkt dieser beiden Linien. Die Temperatur, wo diese Linien schneiden sich die Glasübergangstemperatur. </li><li> Tun Sie dies für alle neun Rampen. </li></ol> 5. Analyse Durchschnittliche Thin Film Dynamics <ol><li> Für eine gegebene Schichtdicke Grundstück Log (Kühlrate (K / min)) gegen 1 / T g (K -1). </li><li> Vergleichen Sie dies indirekt auf Messungen der Masse und Oberflächendynamik durch die empirische Beziehung zu lenken: Kühlrate * τ α = 1000. 23,24 </li></ol>

<ol>
	<li>Keddie, J. L., Jones, R. A. L., Cory, R. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Size-Dependent+depression+of+the+glass+transition+temperature+in+polymer+films.">Size-Dependent depression of the glass transition temperature in polymer films.</a> Europhys. Lett. 27 (1), 59-64 (1994).</li><li>Forrest, J. A., Veress, K. D., Dutcher, J. R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Interface+and+chain+confinement+effects+on+the+glass+transition+temperature+of+thin+polymer+films.">Interface and chain confinement effects on the glass transition temperature of thin polymer films.</a> Phys. Rev.E. 56 (5), 5705-5716 (1997).</li><li>Forrest, J. A., Mattsson, J. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Reductions+of+the+glass+transition+temperature+in+thin+polymer+films:+Probing+the+length+scale+of+cooperative+dynamics.">Reductions of the glass transition temperature in thin polymer films: Probing the length scale of cooperative dynamics.</a> Phys. Rev.E. 61 (1), R53-R56 (2000).</li><li>Sharp, J. S., Forrest, J. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Free+surfaces+cause+reductions+in+the+glass+transition+temperature+of+thin+polystyrene+films.">Free surfaces cause reductions in the glass transition temperature of thin polystyrene films.</a> PRL. 91 (23), 235701 (2003).</li><li>Ellison, C. J., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=The+distribution+of+glass-transition+temperatures+in+nanoscopically+confined+glass+formers.">The distribution of glass-transition temperatures in nanoscopically confined glass formers.</a> Nat. Mat. 2 (10), 695-700 (2003).</li><li>Priestley, R. D., Ellison, C. J., Broadbelt, L. J., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Structural+relaxation+of+polymer+glasses+at+surfaces,+interfaces,+and+in+between.">Structural relaxation of polymer glasses at surfaces, interfaces, and in between.</a> Science. 309 (5733), 456-459 (2005).</li><li>Ellison, C. J., Kim, S. D., Hall, D. B., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Confinement+and+processing+effects+on+glass+transition+temperature+and+physical+aging+in+ultrathin+polymer+films:+Novel+fluorescence+measurements.">Confinement and processing effects on glass transition temperature and physical aging in ultrathin polymer films: Novel fluorescence measurements.</a> Euro. Phys. J. E. 8 (2), 155-166 (2002).</li><li>Ellison, C. J., Mundra, M. K., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Impacts+of+polystyrene+molecular+weight+and+modification+to+the+repeat+unit+structure+on+the+glass+Transition&#8722;Nanoconfinement+effect+and+the+cooperativity+length+scale.">Impacts of polystyrene molecular weight and modification to the repeat unit structure on the glass Transition&#8722;Nanoconfinement effect and the cooperativity length scale.</a> Macromolecules. 38 (5), 1767-1778 (2005).</li><li>Yang, Z., Fujii, Y., Lee, F. K., Lam, C. H., Tsui, O. K. C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glass+transition+dynamics+and+surface+layer+mobility+in+unentangled+polystyrene+films.">Glass transition dynamics and surface layer mobility in unentangled polystyrene films.</a> Science. 328 (5986), 1676-1679 (2010).</li><li>Tsui, O. K. C., Zhang, H. F. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Effects+of+chain+ends+and+chain+entanglement+on+the+glass+transition+temperature+of+polymer+thin+films.">Effects of chain ends and chain entanglement on the glass transition temperature of polymer thin films.</a> Macromolecules. 34 (26), 9139-9142 (2001).</li><li>Roth, C. B., Dutcher, J. R. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glass+Transition+and+Chain+Mobility+in+thin+Polymer+Films.">Glass Transition and Chain Mobility in thin Polymer Films.</a> J. Electroanal. Chem. 584, 13-22 (2005).</li><li>Ediger, M. D., Forrest, J. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Dynamics+near+Free+Surfaces+and+the+Glass+Transition+in+Thin+Polymer+Films:+A+View+to+the+Future.">Dynamics near Free Surfaces and the Glass Transition in Thin Polymer Films: A View to the Future.</a> Macromolecules. 47 (2), 471-478 (2014).</li><li>Serghei, A., Huth, H., Schick, C., Kremer, F. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glassy+dynamics+in+thin+polymer+layers+having+a+free+upper+interface.">Glassy dynamics in thin polymer layers having a free upper interface.</a> Macromolecules. 41 (10), 3636-3639 (2008).</li><li>Huth, H., Minakov, A. A., Schick, C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Differential+AC-chip+calorimeter+for+glass+transition+measurements+in+ultrathin+films.">Differential AC-chip calorimeter for glass transition measurements in ultrathin films.</a> J. Polym. Sci. B. 44 (20), 2996-3005 (2006).</li><li>Tress, M., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glassy+dynamics+in+condensed+isolated+polymer+chains.">Glassy dynamics in condensed isolated polymer chains.</a> Science. 341 (6152), 1371-1374 (2013).</li><li>Boucher, V. M., et al. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=T+g+depression+and+invariant+segmental+dynamics+in+polystyrene+thin+films.">T g depression and invariant segmental dynamics in polystyrene thin films.</a> Soft Matter. 8 (19), 5119-5122 (2012).</li><li>Yu, M., Olson, E. A., Zhang, M., Zhang, Z., Allen, L. H. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glass+transition+in+ultrathin+polymer+films:+Calorimetric+study.">Glass transition in ultrathin polymer films: Calorimetric study.</a> PRL. 91 (8), 085703 (2003).</li><li>Kremer, F., Tress, M., Mapesa, E. U. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Glassy+dynamics+and+glass+transition+in+nanometric+layers+and+films:+A+silver+lining+on+the+horizon.">Glassy dynamics and glass transition in nanometric layers and films: A silver lining on the horizon.</a> J. Non-Crys. Solids. 407, 277-283 (2015).</li><li>Qi, D., Ilton, M., Forrest, J. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Measuring+surface+and+bulk+relaxation+in+glassy+polymers.">Measuring surface and bulk relaxation in glassy polymers.</a> Euro. Phys. J. E. 34 (6), 1-7 (2011).</li><li>Teichroeb, J. H., Forrest, J. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Direct+imaging+of+nanoparticle+embedding+to+probe+viscoelasticity+of+polymer+surfaces.">Direct imaging of nanoparticle embedding to probe viscoelasticity of polymer surfaces.</a> PRL. 91 (1), 016104 (2003).</li><li>Fakhraai, Z., Forrest, J. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Measuring+the+surface+dynamics+of+glassy+polymers.">Measuring the surface dynamics of glassy polymers.</a> Science. 319 (5863), 600-604 (2008).</li><li>Paeng, K., Swallen, S. F., Ediger, M. D. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Direct+measurement+of+molecular+motion+in+freestanding+polystyrene+thin+films.">Direct measurement of molecular motion in freestanding polystyrene thin films.</a> J. Am. Chem. Soc. 133 (22), 8444-8447 (2011).</li><li>Glor, E. C., Fakhraai, Z. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Facilitation+of+interfacial+dynamics+in+entagled+polymer+films.">Facilitation of interfacial dynamics in entagled polymer films.</a> JCP. 141 (9), 194505 (2014).</li><li>Fakhraai, Z., Forrest, J. A. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Probing+slow+dynamics+in+supported+thin+polymer+films.">Probing slow dynamics in supported thin polymer films.</a> PRL. 95 (2), 025701 (2005).</li><li>Roth, C. B., McNerny, K. L., Jager, W. F., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Eliminating+the+enhanced+mobility+at+the+free+surface+of+polystyrene:+fluorescence+studies+of+the+glass+transition+temperature+in+thin+bilayer+films+of+immiscible+polymers.">Eliminating the enhanced mobility at the free surface of polystyrene: fluorescence studies of the glass transition temperature in thin bilayer films of immiscible polymers.</a> Macromolecules. 40 (7), 2568-2574 (2007).</li><li>Priestley, R. D., Ellison, C. J., Broadbelt, L. J., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Structural+relaxation+of+polymer+glasses+at+surfaces,+interfaces,+and+in+between.">Structural relaxation of polymer glasses at surfaces, interfaces, and in between.</a> Science. 309 (5733), 456-459 (2005).</li><li>Gao, S., Koh, Y. P., Simon, S. L. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Calorimetric+Glass+Transition+of+Single+Polystyrene+Ultrathin+Films.">Calorimetric Glass Transition of Single Polystyrene Ultrathin Films.</a> Macromolecules. 46 (92), 562-570 (2013).</li><li>Tropin, T. V., Schulz, G., Schmelzer, J. W. P., Schick, C. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Heat+capacity+measurements+and+modeling+of+polystyrene+glass+transition+in+a+wide+range+of+cooling+rates.">Heat capacity measurements and modeling of polystyrene glass transition in a wide range of cooling rates.</a> J. Non-Cryst. Solids. 409, 63-75 (2015).</li><li>Kim, S., Hewlett, S. A., Roth, C. B., Torkelson, J. M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Confinement+effects+of+glass+transition+temperature,+transition+breadth,+and+expansivity:+Comparison+of+ellipsometry+and+fluorescence+measurements+on+polystyrene+films.">Confinement effects of glass transition temperature, transition breadth, and expansivity: Comparison of ellipsometry and fluorescence measurements on polystyrene films.</a> Eur. Phys. J.E. 30, 83-92 (2009).</li><li>Schawe, J. E. K. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Vitrification+in+a+wide+cooling+rate+range:+The+relations+between+cooling+rate,+relaxation+time,+transition+width+and+fragility.">Vitrification in a wide cooling rate range: The relations between cooling rate, relaxation time, transition width and fragility.</a> JCP. 141, 184905 (2014).</li><li>Donth, E., Korus, J., Hempel, E., Beiner, M. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Comparison+of+DSC+heating+rate+and+HCS+frequency+at+the+glass+transition.">Comparison of DSC heating rate and HCS frequency at the glass transition.</a> Thermochimica Acta. 304-305, 239-249 (1997).</li><li>Zhang, C., Guo, Y., Priestley, R. D. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Confined+glassy+properties+of+polymer+nanoparticles.">Confined glassy properties of polymer nanoparticles.</a> J. Polym. Sci. B. 51 (7), 574-586 (2013).</li><li>Koh, Y. P., Grassia, L., Simon, S. L. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Structural+Recovery+of+a+Single+Polystyrene+Thin+Film+Using+Nanocalorimetry+to+Extend+the+Aging+Time+and+Temperature+Range.">Structural Recovery of a Single Polystyrene Thin Film Using Nanocalorimetry to Extend the Aging Time and Temperature Range.</a> Thermochimica Acta. 603, 135-141 (2015).</li><li>Gao, S., Simon, S. L. <a target="_blank" href="http://www.ncbi.nlm.nih.gov/entrez/query.fcgi?db=PubMed&cmd=Search&doptcmdl=Citation&defaultField=Title+Word&term=Measurement+of+the+limiting+fictive+temperature+over+five+decades+of+cooling+and+heating+rates.">Measurement of the limiting fictive temperature over five decades of cooling and heating rates.</a> Thermochimica Acta. 603, 123-127 (2015).</li></ol>

The Authors have no conflicts of interest to disclose.

Cooling-Rate abhängig Tg Messungen mit hohem Durchsatz Experimente zur Charakterisierung, die die T g, die Ausdehnungskoeffizienten des Glases und der unterkühlten Flüssigkeit, die Temperaturabhängigkeit der durchschnittliche Dynamik und die Zerbrechlichkeit eines bestimmten glasartiges Material in einer bestimmen kann, einzigen Experiment. Darüber hinaus, im Gegensatz zu Fluoreszenz, Einbetten oder nanohole Relaxationsexperimente sind CR-T g Experimenten relativ schnell und einfach...

Die bahnbrechenden Arbeiten von Keddie Jones und Corey 1 zeigten, dass die Glasübergangstemperatur (Tg) von ultra-dünnen Polystyrol-Folien in Bezug auf die Volumenwert bei einer Dicke von weniger als 60 nm abnimmt. Seitdem wurden viele experimentelle Studien 2-11 die Hypothese, daß die beobachtete Verringerung der T g sind durch eine Schicht aus verbesserte Mobilität in der Nähe der freien Oberfläche dieser Filme verursacht unterstützt. Jedoch sind diese Versuche sind indirekte Maßnahmen einer einzigen Relaxationszeit und somit gibt es eine Diskussion 12- 18, die auf eine direkte Korrelation zwischen den durchschnittlichen Dünnschicht Dynamik und der Dynamik an der Luft / Polymer-Grenzfläche zentriert ist. Um diese Debatte zu beantworten, haben viele Studien direkt die Dynamik der freien Oberfläche (τ Oberfläche) gemessen. Nanopartikel-Einbettung, 19,20 nanohole Entspannung, 21 und Fluoreszenz 22 Studien zeigen, dass das Luft / Polymer-Grenzfläche hals Dynamik Größenordnungen schneller als die Masse alpha Relaxationszeit (τ α) mit einer viel schwächeren Temperaturabhängigkeit als die von τ α. Wegen seiner schwachen Temperaturabhängigkeit der τ Oberfläche dieser Filme, 19-22 und verbesserte Dynamik der dünnen Polystyrolfilme, 23,24 schneidet den Massen alpha Entspannung (τ α) an einem einzigen Punkt T *, die ein paar Grad über ist T g, und bei einem τ α von ≈ 1 sec. Die Anwesenheit von T * könnte erklären, warum Versuche, die Relaxationszeiten Sonde schneller als * versäumen, eine Dicke Abhängigkeit von der T g von ultra-dünnen Polystyrol-Filme zu sehen. 13-18 Schließlich, während direkte Messungen der verstärkten mobilen Schicht zeigen, dass es eine Dicke von 4-8 nm, 20-22 gibt es Hinweise, dass die Ausbreitungslänge der Dynamik an der Luft / Polymer-Grenzfläche ist wesentlich größer als die Dicke der zu bewegenden Fläche layer. 5,25,26 Dieser Bericht soll vollständig zu beschreiben, ein Protokoll für die Verwendung von Ellipsometrie für Kühlgeschwindigkeit abhängigen T g (CR-T g) Experimente. CR-T g wurden zuvor verwendet, um die durchschnittliche Dynamik von ultradünnen Folien aus Polystyrol zu beschreiben. 23,24,27,28 Weiterhin wurde diese Technik kürzlich verwendet, um eine direkte Korrelation zwischen den durchschnittlichen Dynamik in ultradünnen Polystyrolfilme zeigen und die Dynamik an der freien Oberfläche. 23 Der Vorteil der CR-Tg-Messungen gegenüber anderen Arten von Messungen, wie Fluoreszenz, Nanopartikel-Einbettung, nanohole Entspannung, nanocalorimetry, dielektrische Spektroskopie und Brillouin-Lichtstreuung, ist Studien, dass sie relativ schnell sind und einfachen Experimenten, die nicht zu nutzen weiß Fluorophore oder andere komplizierte experimentelle Techniken. Jüngste Fortschritte in der spektroskopischen Ellipsometrie ermöglicht diese Technik verwendet werden, um die optische propert effizient bestimmen,ies von ultradünnen Folien aus Polymeren und andere Arten von Hybridmaterialien mit außergewöhnlicher Genauigkeit. Als solche sind die Sonden dieser Technik wird die durchschnittliche Dynamik technologisch anwendbar Dünnschichten in der Temperatur und Zeitregime, die für die Glasübergangs (T ≤ T g, τ α ≥ 100 s). Darüber hinaus wird diese Technik Informationen zu den Ausdehnungskoeffizienten der glasartigen geben und Abendessen gekühlte Flüssigkeit Staaten sowie die Fragilität des Systems, die dann mit den Daten für Groß Filmen verglichen werden kann. Schließlich kann CR- Tg Experimenten für jede glasartige System, solange die Integrität des Films während des gesamten Versuchs bleibt verwendet werden.

<table><tbody><tr><td>Toluene</td><td>Sigma Aldrich</td><td>179418-1L</td><td>This can be purchased from any chemical company.</td></tr><tr><td>Atactic Polystyrene</td><td>Polymer Source Inc.</td><td>P-4092-S</td><td>This can be purchased from any chemical company.</td></tr><tr><td>THMS 600 temperature stage</td><td>Linkam</td><td>THMS 600</td><td>any temperature stage that can be fit to an ellipsometer could be used.</td></tr><tr><td>M2000V Spectroscopic Ellipsometer</td><td>J.A. Woollam</td><td>M200V</td><td>This procedure should be applicable for any spectroscopic ellipsometer.</td></tr><tr><td>Spin Coater</td><td>Laurell Technologies</td><td>WS-650-23B</td><td>This Procedure is possible with any spin coater</td></tr><tr><td>Sample vials</td><td>Fisher Scientific</td><td>02-912-379</td><td>Any sample vials will do</td></tr><tr><td>Silicon wafers</td><td>Virginia semi conductors</td><td>325S1410694D</td><td></td></tr></tbody></table>

cooling rate dependent ellipsometry measurements to determine the dynamics of thin glassy films

Dieser Bericht soll vollständig zu beschreiben, die experimentelle Technik der Verwendung von Ellipsometrie für Kühlgeschwindigkeit abhängigen T g (CR-T g) Experimente. Diese Messungen sind einfache Hochdurchsatz-Experimente zur Charakterisierung, die die Glasübergangstemperatur zu bestimmen können (T g), mittlere Dynamik, Zerbrechlichkeit und die Ausdehnungskoeffizienten der unterkühlten Flüssigkeit und glasig Zustände für eine Vielzahl von glasartigen Materialien. Diese Technik ermöglicht diese Parameter in einem einzigen Experiment bestimmt werden, während andere Verfahren müssen eine Vielzahl von verschiedenen Techniken zu kombinieren, um alle diese Eigenschaften zu untersuchen. Messungen der Dynamik zu schließen, um T g sind besonders anspruchsvoll. Der Vorteil der Abkühlgeschwindigkeit abhängt Tg-Messungen gegenüber anderen Verfahren, die direkt untersuchen Volumen- und Oberflächen Relaxationsdynamik ist, dass sie relativ schnell und einfach Versuche, die nicht Fluorophore oder andere komplizierte ex nutzen liegenexperimentelle Techniken. Ferner tastet diese Technik die durchschnittliche Dynamik der technisch relevanten Dünnschichten in der Temperatur und Relaxationszeit (τ α) Rahmenbedingungen, die für die Glasübergangs (τ α&gt; 100 s). Die Beschränkung auf mit Ellipsometrie für Kühlgeschwindigkeit abhängigen T g Experimenten ist, dass es nicht die Sonde kann Relaxationszeiten relevanten Messungen der Viskosität (τ α &lt;&lt; 1 sec). Andere Kühlgeschwindigkeit abhängigen T g Messverfahren kann jedoch die CR-T g Methode schneller Relaxationszeiten zu verlängern. Darüber hinaus kann diese Technik für alle glasartigen Systems, solange die Integrität des Films während des gesamten Versuchs bleibt verwendet werden.

Fitting Raw Ellipsometry Daten Polystyrolfolien sind im Wellenlängenbereich des Ellipsometers (500-1,600 nm). Somit eine Cauchy-Modell ist ein gutes Modell für den Brechungsindex der Polystyrol-Folien beschreibt. 1A zeigt ein Beispiel Ψ (λ) und Δ (λ) für eine Dicke (274 nm) Film aus Polystyrol, und die daraus resultierende Anpassung an die Cauchy-Modell <img alt="Gleichung 1" src="/file...

Watch this Scientific Journal Video about Cooling Rate Dependent Ellipsometry Measurements to Determine the Dynamics of Thin Glassy Films at JoVE.com

Cooling Rate Dependent Ellipsometry Measurements to Determine the Dynamics of Thin Glassy Films

Hier stellen wir ein Protokoll für die Kühlrate abhängig Ellipsometrie Experimente, die die Glasübergangstemperatur (T g) bestimmen kann, die durchschnittliche Dynamik, Zerbrechlichkeit und die Ausdehnungskoeffizienten der unterkühlten Flüssigkeit und Glas für eine Vielzahl von glasartigen Materialien.

Kühlrate Dependent Ellipsometriemessungen die Dynamik des Thin Glassy Films zu ermitteln

This report aims to fully describe the experimental technique of using ellipsometry for cooling rate dependent Tg (CR-Tg) experiments. These measurements ...

cooling-rate-dependent-ellipsometry-measurements-to-determine

Universidad de Cartagena UDEC

Research

JoVE Journal

Chemistry

8.1K Aufrufe.  University of Pennsylvania.  Hier stellen wir ein Protokoll für die Kühlrate abhängig Ellipsometrie Experimente, die die Glasübergangstemperatur (T g) bestimmen kann, die durchschnittliche Dynamik, Zerbrechlichkeit und die Ausdehnungskoeffizienten der unterkühlten Flüssigkeit und Glas für eine Vielzahl von glasartigen Materialien. 

Serie: Cooling Rate Dependent Ellipsometry Measurements to Determine the Dynamics of Thin Glassy Films

High-resolution Thermal Micro-imaging Using Europium Chelate Luminescent Coatings

Micro-electronic devices often undergo significant self-heating when biased to their typical operating conditions. This paper describes a convenient optical micro-imaging technique which can be used to map and quantify such behavior. Europium thenoyltrifluoroacetonate (EuTFC) has a 612 nm luminescence line whose activation efficiency drops strongly with increasing temperature, due to T-dependent interactions between the Eu3+ ion and the organic chelating compound. This material may be readily coated on to a sample surface by thermal sublimation in vacuum. When the coating is excited with ultraviolet light (337 nm) an optical micro-image of the 612 nm luminescent response can be converted directly into a map of the sample surface temperature. This technique offers spatial resolution limited only by the microscope optics (about 1 micron) and time resolution limited by the speed of the camera employed. It offers the additional advantages of only requiring comparatively simple and non-specialized equipment, and giving a quantitative probe of sample temperature.

Europium thenoyltrifluoroacetonate (EuTFC) has an optical luminescence line at 612 nm, whose activation efficiency decreases strongly with temperature. If a sample coated with a thin film of this material is micro-imaged, the 612 nm luminescent response intensity may be converted into a direct map of sample surface temperature.

Hochauflösende Thermal Micro-Bildgebung Europiumchelatlösung Lumineszente Coatings

Micro-electronic devices often undergo significant self-heating when biased to their typical operating conditions. This paper describes a convenient ...

Forschung

Ingenieurwesen

Evanescent Field Based Photoacoustics: Optical Property Evaluation at Surfaces

Here, we present a protocol to estimate material and surface optical properties using the photoacoustic effect combined with total internal reflection. Optical property evaluation of thin films and the surfaces of bulk materials is an important step in understanding new optical material systems and their applications. The method presented can estimate thickness, refractive index, and use absorptive properties of materials for detection. This metrology system uses evanescent field-based photoacoustics (EFPA), a field of research based upon the interaction of an evanescent field with the photoacoustic effect. This interaction and its resulting family of techniques allow the technique to probe optical properties within a few hundred nanometers of the sample surface. This optical near field allows for the highly accurate estimation of material properties on the same scale as the field itself such as refractive index and film thickness. With the use of EFPA and its sub techniques such as total internal reflection photoacoustic spectroscopy (TIRPAS) and optical tunneling photoacoustic spectroscopy (OTPAS), it is possible to evaluate a material at the nanoscale in a consolidated instrument without the need for many instruments and experiments that may be cost prohibitive.

Here we present a protocol to estimate material and surface optical properties using the photoacoustic effect combined with total internal reflection. This technique evanescent field-based photoacoustics can be used to create a photoacoustic metrology system to estimate materials&#39; thicknesses, bulk and thin film refractive indices, and explore their optical properties.

Abklingende Feld Basierend Photoakustik: Optische Objektbewertung an Oberflächen

Here, we present a protocol to estimate material and surface optical properties using the photoacoustic effect combined with total internal reflection. ...

Electrospray Deposition of Uniform Thickness Ge23Sb7S70 and As40S60 Chalcogenide Glass Films

Solution-based electrospray film deposition, which is compatible with continuous, roll-to-roll processing, is applied to chalcogenide glasses. Two chalcogenide compositions are demonstrated: Ge23Sb7S70 and As40S60, which have both been studied extensively for planar mid-infrared (mid-IR) microphotonic devices. In this approach, uniform thickness films are fabricated through the use of computer numerical controlled (CNC) motion. Chalcogenide glass (ChG) is written over the substrate by a single nozzle along a serpentine path. Films were subjected to a series of heat treatments between 100 &#176;C and 200 &#176;C under vacuum to drive off residual solvent and densify the films. Based on transmission Fourier transform infrared (FTIR) spectroscopy and surface roughness measurements, both compositions were found to be suitable for the fabrication of planar devices operating in the mid-IR region. Residual solvent removal was found to be much quicker for the As40S60 film as compared to Ge23Sb7S70. Based on the advantages of electrospray, direct printing of a gradient refractive index (GRIN) mid-IR transparent coating is envisioned, given the difference in refractive index of the two compositions in this study.

Electrospray Deposition of Uniform Thickness Ge23Sb7S70 and As40S60 Chalcogenide Glass Films

A method of uniform thickness solution-derived chalcogenide glass film deposition is demonstrated using computer numerical controlled motion of a single-nozzle electrospray.

Elektroabscheidung von einheitlicher Dicke Ge<sub&gt; 23</sub&gt; Sb<sub&gt; 7</sub&gt; S<sub&gt; 70</sub&gt; Und As<sub&gt; 40</sub&gt; S<sub&gt; 60</sub&gt; Chalkogenidglases Films

Solution-based electrospray film deposition, which is compatible with continuous, roll-to-roll processing, is applied to chalcogenide glasses. Two ...

Recombination Dynamics in Thin-film Photovoltaic Materials via Time-resolved Microwave Conductivity

A method for investigating recombination dynamics of photo-induced charge carriers in thin film semiconductors, specifically in photovoltaic materials such as organo-lead halide perovskites is presented. The perovskite film thickness and absorption coefficient are initially characterized by profilometry and UV-VIS absorption spectroscopy. Calibration of both laser power and cavity sensitivity is described in detail. A protocol for performing Flash-photolysis Time Resolved Microwave Conductivity (TRMC) experiments, a non-contact method of determining the conductivity of a material, is presented. A process for identifying the real and imaginary components of the complex conductivity by performing TRMC as a function of microwave frequency is given. Charge carrier dynamics are determined under different excitation regimes (including both power and wavelength). Techniques for distinguishing between direct and trap-mediated decay processes are presented and discussed. Results are modelled and interpreted with reference to a general kinetic model of photoinduced charge carriers in a semiconductor. The techniques described are applicable to a wide range of optoelectronic materials, including organic and inorganic photovoltaic materials, nanoparticles, and conducting/semiconducting thin films.

A Time Resolved Microwave Conductivity technique for investigating direct and trap-mediated recombination dynamics and determining carrier mobilities of thin film semiconductors is presented here.

Rekombinationsdynamik in Dünnschicht-Photovoltaik-Materialien über zeitaufgelöste Mikrowellenleitfähigkeit

A method for investigating recombination dynamics of photo-induced charge carriers in thin film semiconductors, specifically in photovoltaic materials ...

Orientational Transition in a Liquid Crystal Triggered by the Thermodynamic Growth of Interfacial Wetting Sheets

In liquid crystal (LC) physical chemistry, molecules near the surface play a great role in controlling bulk orientation. Thus far, mainly to achieve desired molecular orientation states in LC displays, the "static" surface property of LCs, so-called surface anchoring, has been intensively studied. As a rule of thumb, once the initial orientation of LCs is "locked" by specific surface treatments, such as rubbing or treatment with a specific alignment layer, it hardly changes with temperature. Here, we present a system exhibiting an orientational transition upon temperature variation, which conflicts with the consensus. Right on the transition, the bulk LC molecules experience the orientational rotation, with 90&#176; between the planar (P) orientation at high temperatures and the vertical (V) orientation at low temperatures in the first-order transitional manner. We have tracked thermodynamic surface anchoring behavior by means of polarizing optical microscopy (POM), dielectric spectroscopy (DS), high-resolution differential scanning calorimetry (HR-DSC), and grazing incidence X-ray diffraction (GI-XRD) and reached a plausible physical explanation: that the transition is triggered by a growth of surface wetting sheets, which impose the V orientation locally against the P orientation in the bulk. This landscape would provide a general link explaining how the equilibrium bulk orientation is affected by surface-localized orientation in many LC systems. In our characterization, POM and DS are advantageous by offering information on the spatial distribution of the orientation of LC molecules. HR-DSC gives information about the precise thermodynamic information on transitions, which cannot be addressed by conventional DSC instruments due to limited resolution. GI-XRD provides information on surface-specific molecular orientation and short-range orderings. The goal of this paper is to present a protocol for preparing a sample that exhibits the transition and to demonstrate how the thermodynamic structural variation, both in the bulk and on surfaces, can be analyzed through the abovementioned methods.

Here, we present a protocol to trigger an orientational transition of a liquid crystal in response to temperature. Methodologies are described for preparing a sample in order to observe the transition and the detailed transitional evolution.

Orientationaler Übergang in einem Flüssigkristall, der durch das thermodynamische Wachstum von Grenzflächenbetonplatten ausgelöst wird

In liquid crystal (LC) physical chemistry, molecules near the surface play a great role in controlling bulk orientation. Thus far, mainly to achieve ...

Preparation of Liquid Crystal Networks for Macroscopic Oscillatory Motion Induced by Light

A strategy based on doped liquid crystalline networks is described to create mechanical self-sustained oscillations of plastic films under continuous light irradiation. The photo-excitation of dopants that can quickly dissipate light into heat, coupled with anisotropic thermal expansion and self-shadowing of the film, gives rise to the self-sustained deformation. The oscillations observed are influenced by the dimensions and the modulus of the film, and by the directionality and intensity of the light. The system developed offers applications in energy conversion and harvesting for soft-robotics and automated systems.
The general method described here consists of creating free-standing liquid crystalline films and characterizing the mechanical and thermal effects observed. The molecular alignment is achieved using alignment layers (rubbed polyimide), commonly used in the display manufacturing industry. To obtain actuators with large deformation, the mesogens are aligned and polymerized in a splay/bend configuration, i.e., with the director of the liquid crystals (LCs) going gradually from planar to homeotropic through the film thickness. Upon irradiation, the mechanical and thermal oscillations obtained are monitored with a high-speed camera. The results are further quantified by image analysis using an image processing program.

The goal of the protocol is to create liquid crystalline polymer films that can mechanically oscillate under continuous light irradiation. We describe in great detail the conception of free-standing films, from the liquid crystal alignment method to the photo-actuation. The experimental protocol applied to prepare this material is broadly applicable.

Vorbereitung der Flüssigkristall-Netzwerke für makroskopische oszillierende Bewegung, die durch Licht induzierten

A strategy based on doped liquid crystalline networks is described to create mechanical self-sustained oscillations of plastic films under continuous ...

Bulk and Thin Film Synthesis of Compositionally Variant Entropy-stabilized Oxides

Here, we present a procedure for the synthesis of bulk and thin film multicomponent (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (Co variant) and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O (Cu variant) entropy-stabilized oxides. Phase pure and chemically homogeneous (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (x = 0.20, 0.27, 0.33) and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O (x = 0.11, 0.27) ceramic pellets are synthesized and used in the deposition of ultra-high quality, phase pure, single crystalline thin films of the target stoichiometry. A detailed methodology for the deposition of smooth, chemically homogeneous, entropy-stabilized oxide thin films by pulsed laser deposition on (001)-oriented MgO substrates is described. The phase and crystallinity of bulk and thin film materials are confirmed using X-ray diffraction. Composition and chemical homogeneity are confirmed by X-ray photoelectron spectroscopy and energy dispersive X-ray spectroscopy. The surface topography of thin films is measured with scanning probe microscopy. The synthesis of high quality, single crystalline, entropy-stabilized oxide thin films enables the study of interface, size, strain, and disorder effects on the properties in this new class of highly disordered oxide materials.

The synthesis of high quality bulk and thin film (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O and (Mg0.25(1-x)Co0.25(1-x)Ni0.25(1-x)CuxZn0.25(1-x))O entropy-stabilized oxides is presented.

Bulk- und Dünnschicht-Synthese von kompositorisch Variante Entropie-stabilisierten Oxide

Here, we present a procedure for the synthesis of bulk and thin film multicomponent (Mg0.25(1-x)CoxNi0.25(1-x)Cu0.25(1-x)Zn0.25(1-x))O (Co variant) and ...

Film Control to Study Contributions of Waves to Droplet Impact Dynamics on Thin Flowing Liquid Films

Droplet impact is a very common phenomenon in nature and attracts attention due to its aesthetic fascination and wide-ranging applications. Previous studies on flowing liquid films have neglected the contributions of spatial structures of waves to the impact outcome, while this has recently been shown to have a significant influence on the drop impact dynamics. In this report, we outline a step-by-step procedure to investigate the effect of periodic inlet forcing of a flowing liquid film leading to the production of spatiotemporally regular wave structures on drop impact dynamics. A function generator in connection with a solenoid valve is used to excite these spatiotemporally regular wave structures on the film surface while the impact dynamics of uniform-sized droplets are captured using a high-speed camera. Three distinct regions are then studied; viz. the capillary wave region preceding the large wave peak, the flat film region, and the wave hump region. The effects of important dimensionless quantities such as film Reynolds, drop Weber and Ohnesorge numbers parameterized by the film flow rate, drop speed, and drop size are also examined. Our results show interesting, hitherto undiscovered dynamics brought about by this application of film inlet forcing of the flowing film for both low and high inertia drops.

A protocol to study the contributions of waves to droplet impact dynamics on flowing liquid films is presented.

Film-Kontrolle, Beiträge der Wellen zu Tröpfchen Auswirkungen Dynamik auf dünnen fließt Flüssigkeitsfilme zu studieren

Droplet impact is a very common phenomenon in nature and attracts attention due to its aesthetic fascination and wide-ranging applications. Previous ...

Thin Film Composite Silicon Elastomers for Cell Culture and Skin Applications: Manufacturing and Characterization

In this protocol, we present methods to fabricate thin elastomer composite films for advanced cell culture applications and for the development of skin adhesives. Two different poly-(dimethyl siloxanes) (PDMS and soft skin adhesive (SSA)), have been used for in depth investigation of biological effects and adhesive characteristics. The composite films consist of a flexible backing layer and an adhesive top coating. Both layers have been manufactured by doctor blade application technique. In the present investigation, the adhesive behavior of the composite films has been investigated as a function of the layer thickness or a variation of the Young&#39;s modulus of the top layer. The Young&#39;s modulus of PDMS has been changed by varying the base to crosslinker mixing ratio. In addition, the thickness of SSA films has been varied from approx. 16 &#181;m to approx. 320 &#181;m. Scanning electron microscopy (SEM) and optical microscopy have been used for thickness measurements. The adhesive properties of elastomer films depend strongly on the film thickness, the Young&#39;s modulus of the polymers and surface characteristics. Therefore, normal adhesion of these films on glass substrates exhibiting smooth and rough surfaces has been investigated. Pull-off stress and work of separation are dependent on the mixing ratio of silicone elastomers.
Additionally, the thickness of the soft skin adhesive placed on top of a supportive backing layer has been varied in order to produce patches for skin applications. Cytotoxicity, proliferation and cellular adhesion of L929 murine fibroblasts on PDMS films (mixing ratio 10:1) and SSA films (mixing ratio 50:50) have been conducted. We have shown here, for the first time, the side by side comparison of thin composite films manufactured of both polymers and present the investigation of their biological- and adhesive properties.

A protocol for the manufacturing process of polymeric thin film composite structures possessing either different Young&#39;s moduli or thicknesses is presented. Films are produced for advanced cell culture studies or as skin adhesives.

Dünnen Film Composite Silikon Elastomere für Zellkultur und Haut Anwendungen: Herstellung und Charakterisierung

In this protocol, we present methods to fabricate thin elastomer composite films for advanced cell culture applications and for the development of skin ...

Entwicklungsbiologie

High-Contrast and Fast Photorheological Switching of a Twist-Bend Nematic Liquid Crystal

Smart viscoelastic materials that respond to specific stimuli are one of the most attractive classes of materials important to future technologies, such as on-demand switchable adhesion technologies, actuators, molecular clutches, and nano-/microscopic mass transporters. Recently it was found that through a special solid-liquid transition, rheological properties can exhibit significant changes, thus providing suitable smart viscoelastic materials. However, designing materials with such a property is complex, and forward and backward switching times are usually long. Therefore, it is important to explore new working mechanisms to realize solid-liquid transitions, shorten the switching time, and enhance the contrast of rheological properties during switching. Here, a light-induced crystal-liquid phase transition is observed, which is characterized by means of polarizing light microscopy (POM), photorheometry, photo-differential scanning calorimetry (photo-DSC), and X-ray diffraction (XRD). The light-induced crystal-liquid phase transition presents key features such as (1) fast switching of crystal-liquid phases for both forward and backward reactions and (2) a high contrast ratio of viscoelasticity. In the characterization, POM is advantageous in offering information on the spatial distribution of LC molecule orientations, determining the type of liquid crystalline phases appearing in the material, and studying the orientation of LCs. Photorheometry allows measurement of a material&#8217;s rheological properties under light stimuli and can reveal the photorheological switching properties of materials. Photo-DSC is a technique to investigate thermodynamic information of materials in darkness and under light irradiation. Lastly, XRD allows studying of microscopic structures of materials. The goal of this article is to clearly present how to prepare and measure the discussed properties of a photorheological material.

This protocol demonstrates the preparation of a photorheological material that exhibits a solid phase, various liquid crystalline phases, and an isotropic liquid phase by increasing temperature. Presented here are methods for measuring the structure-viscoelasticity relationship of the material.

Kontrastreich und schnelles photorheologisches Schalten eines Twist-Bend Nematic Flüssigkristalls

Smart viscoelastic materials that respond to specific stimuli are one of the most attractive classes of materials important to future technologies, such ...