Synthesis and surface modification of semiconductor nanocrystals

The last decade has witnessed an exponential growth of activities in the field of nanoscience and nanotechnology worldwide, driven both by the excitement of understanding new science and by the potential hope for applications and economic impacts. The largest activity in this field up to date has been in the synthesis and characterization of new materials consisting of particles with dimensions in the order of a few nanometers, so-called nanocrystalline materials. [1-8] Semiconductor nanomaterials such as III/V or II/VI compound semiconductors exhibit strong quantum confinement behavior in the size range from 1 to 10 nm. Therefore, preparation of high quality semiconductor nanocrystals has been a challenge for synthetic chemists, leading to the recent rapid progress in delivering a wide variety of semiconducting nanomaterials. Semiconductor nanocrystals, also called quantum dots, possess physical properties distinctly different from those of the bulk material. Typically, in the size range from 1 to 10 nm, when the particle size is changed, the band gap between the valence and the conduction band will change, too. In a simple approximation a particle in a box model has been used to describe the phenomenon[9]: at nanoscale dimensions the degenerate energy states of a semiconductor separate into discrete states and the system behaves like one big molecule. The size-dependent transformation of the energy levels of the particles is called “quantum size-effect”. Quantum confinement of both the electron and hole in all three dimensions leads to an increase in the effective bandgap of the material with decreasing crystallite size. Consequently, both the optical absorption and emission of semiconductor nanaocrystals shift to the blue (higher energies) as the size of the particles gets smaller. This color tuning is well documented for CdSe nanocrystals whose absorption and emission covers almost the whole visible spectral range. As particle sizes become smaller the ratio of surface atoms to those in the interior increases, which has a strong impact on particle properties, too. Prominent examples are the low melting point [8] and size/shape dependent pressure resistance [10] of semiconductor nanocrystals. Given the size dependence of particle properties, chemists and material scientists now have the unique opportunity to change the electronic and chemical properties of a material by simply controlling the particle size. In particular, CdSe nanocrystals have been widely investigated. Mainly due to their size-dependent optoelectronic properties [11, 12] and flexible chemical processibility [13], they have played a distinguished role for a number of seminal studies [11, 12, 14, 15]. Potential technical applications have been discussed, too. [8, 16-27] Improvement of the optoelectronic properties of semiconductor nanocrystals is still a prominent research topic. One of the most important approaches is fabricating composite type-I core-shell structures which exhibit improved properties, making them attractive from both a fundamental and a practical point of view. Overcoating of nanocrystallites with higher band gap inorganic materials has been shown to increase the photoluminescence quantum yields by eliminating surface nonradiative recombination sites. [28] Particles passivated with inorganic shells are more robust than nanocrystals covered by organic ligands only and have greater tolerance to processing conditions necessary for incorporation into solid state structures or for other applications. Some examples of core-shell nanocrystals reported earlier include CdS on CdSe [29], CdSe on CdS, [30], ZnS on CdS, [31] ZnS on CdSe[28, 32], ZnSe on CdSe [33] and CdS/HgS/CdS [34]. The characterization and preparation of a new core-shell structure, CdSe nanocrystals overcoated by different shells (CdS, ZnS), is presented in chapter 4. Type-I core-shell structures as mentioned above greatly improve the photoluminescence quantum yield and chemical and photochemical stability of nanocrystals. The emission wavelengths of type-I core/shell nanocrystals typically only shows a small red-shift when compared to the plain core nanocrystals. [30, 31, 35] In contrast to type-I core-shell nanocrystals, only few studies have been conducted on colloidal type-II core/shell structures [36-38] which are characterized by a staggered alignment of conduction and valence bands giving rise to a broad tunability of absorption and emission wavelengths, as was shown for CdTe/CdSe core-shell nanocrystals. [36] The emission of type-II core/shell nanocrystals mainly originates from the radiative recombination of electron-hole pairs across the core-shell interface leading to a long photoluminescence lifetime. Type-II core/shell nanocrystals are promising with respect to photoconduction or photovoltaic applications as has been discussed in the literature.[39] Novel type-II core-shell structures with ZnTe cores are reported in chapter 5. The recent progress in the shape control of semiconductor nanocrystals opens new fields of applications. For instance, rod shaped CdSe nanocrystals can enhance the photo-electro conversion efficiency of photovoltaic cells, [40, 41] and also allow for polarized emission in light emitting diodes. [42, 43] Shape control of anisotropic nanocrystals can be achieved by the use of surfactants, [44, 45] regular or inverse micelles as regulating agents, [46, 47] electrochemical processes, [48] template-assisted [49, 50] and solution-liquid-solution (SLS) growth mechnism. [51-53] Recently, formation of various CdSe nanocrystal shapes has been reported by the groups of Alivisatos [54] and Peng, [55] respectively. Furthermore, it has been reported by the group of Prasad [56] that noble metal nanoparticles can induce anisotropic growth of CdSe nanocrystals at lower temperatures than typically used in other methods for preparing anisotropic CdSe structures. Although several approaches for anisotropic crystal growth have been reported by now, developing new synthetic methods for the shape control of colloidal semiconductor nanocrystals remains an important goal. Accordingly, we have attempted to utilize a crystal phase control approach for the controllable synthesis of colloidal ZnE/CdSe (E = S, Se, Te) heterostructures in a variety of morphologies. The complex heterostructures obtained are presented in chapter 6. The unique optical properties of nanocrystals make them appealing as in vivo and in vitro fluorophores in a variety of biological and chemical investigations, in which traditional fluorescence labels based on organic molecules fall short of providing long-term stability and simultaneous detection of multiple emission colours [References]. The ability to prepare water soluble nanocrystals with high stability and quantum yield has led to promising applications in cellular labeling, [57, 58] deep-tissue imaging, [59, 60] and assay labeling [61, 62]. Furthermore, appropriately solubilized nanocrystals have been used as donors in fluorescence resonance energy transfer (FRET) couples. [63-65] Despite recent progress, much work still needs to be done to achieve reproducible and robust surface functionalization and develop flexible (bio-) conjugation techniques. Based on multi-shell CdSe nanocrystals, several new solubilization and ligand exchange protocols have been developed which are presented in chapter 7. The organization of this thesis is as follows: A short overview describing synthesis and properties of CdSe nanocrystals is given in chapter 2. Chapter 3 is the experimental part providing some background information about the optical and analytical methods used in this thesis. The following chapters report the results of this work: synthesis and characterization of type-I multi-shell and type-II core/shell nanocrystals are described in chapter 4 and chapter 5, respectively. In chapter 6, a high–yield synthesis of various CdSe architectures by crystal phase control is reported. Experiments about surface modification of nanocrystals are described in chapter 7. At last, a short summary of the results is given in chapter 8.

Analyse der Funktion von Dystroglycan im frühen sich entwickelnden ZNS mittels inhibierender Antikörper

In der vorliegenden Arbeit wurde die Funktion von Dystroglycan in jungen und späten Stadien des sich entwickelnden ZNS untersucht. Hierzu wurden Antikörper generiert, die fähig waren, in vivo die Interaktion zwischen a-und b-Dystroglycan zu stören. Die Antikörper oder Fab-Fragmente wurden in das Mesencephalon oder Auge lebender Hühnerembryonen injiziert, um aus den beobachteten Veränderungen die Funktion des DAG zu untersuchen. Die Fab-Fragmentinjektionen führten zu Hyperproliferation, verbunden mit morphologischen Veränderungen der Neuroepithelzellen und Zunahme der Anzahl postmitotischer Neuronen. Ebenso wurde die basale und apikale Polarität von Neuroepithelzellen beeinflusst. Auch die Axonorientierung der tectobulbären Axone wurde durch die Injektionen gestört. In älteren embryonalen Stadien kam es, durch Fab-Fragmentinjektionen in die Augen von Embryonen, zu strukturellen Veränderungen der Retina, verbunden mit einer breiteren Verteilung des DAG, wie auch der Synapsen innerhalb der OPL. Die retinalen Zelltypen, wie Müller-Gliazellen und Stäbchen-Bipolarzellen, waren abgerundet und hatten ihre typische Zellform verloren. Die Ergebnisse dieser Arbeit zeigen, dass Dystroglycan einen entscheidenden Einfluss auf die Proliferation, Migration, Polarität und Differenzierung der Neuroepithelzellen ausübt. Außerdem zeigen diese Daten, dass Dystroglycan nicht nur in der frühen embryonalen ZNS-Entwicklung eine maßgebliche Rolle spielt, sondern auch in späten Stadien. Die Ähnlichkeit der beobachteten Veränderungen nach Fab-Fragmentinjektionen legt nahe, dass einige Veränderungen im ZNS bestimmter Muskeldystrophieformen, durch Beeinflussung der Neuroepithelzellen im sich entwickelnden ZNS, verursacht werden.

Quantum dot-dye hybrid systems for energy transfer applications

In this thesis, we focus on the preparation of energy transfer-based quantum dot (QD)-dye hybrid systems. Two kinds of QD-dye hybrid systems have been successfully synthesized: QD-silica-dye and QD-dye hybrid systems.rn rnIn the QD-silica-dye hybrid system, multishell CdSe/CdS/ZnS QDs were adsorbed onto monodisperse Stöber silica particles with an outer silica shell of thickness 2 - 24 nm containing organic dye molecules (Texas Red). The thickness of this dye layer has a strong effect on the total sensitized acceptor emission, which is explained by the increase in the number of dye molecules homogeneously distributed within the silica shell, in combination with an enhanced surface adsorption of QDs with increasing dye amount. Our conclusions were underlined by comparison of the experimental results with Monte-Carlo simulations, and by control experiments confirming attractive interactions between QDs and Texas Red freely dissolved in solution. rnrnNew QD-dye hybrid system consisting of multishell QDs and organic perylene dyes have been synthesized. We developed a versatile approach to assemble extraordinarily stable QD-dye hybrids, which uses dicarboxylate anchors to bind rylene dyes to QD. This system yields a good basis to study the energy transfer between QD and dye because of its simple and compact design: there is no third kind of molecule linking QD and dye; no spacer; and the affinity of the functional group to the QD surface is strong. The FRET signal was measured for these complexes as a function of both dye to QD ratio and center-to-center distance between QD and dye by controlling number of covered ZnS layers. Data showed that fluorescence resonance energy transfer (FRET) was the dominant mechanism of the energy transfer in our QD-dye hybrid system. FRET efficiency can be controlled by not only adjusting the number of dyes on the QD surface or the QD to dye distance, but also properly choosing different dye and QD components. Due to the strong stability, our QD-dye complexes can also be easily transferred into water. Our approach can apply to not only dye molecules but also other organic molecules. As an example, the QDs have been complexed with calixarene molecules and the QD-calixarene complexes also have potential for QD-based energy transfer study. rn

Synthese und Evaluierung von [18 F]-Fluormethyltosylat als prosthetische Gruppe für die 18 F-Fluormethylierung von ZNS-Liganden für die PET

Die 11C-Methylierung von Radioliganden ist eine weit verbreitete Markierungsstrategie für PET-Liganden. Aber die kurze Halbwertszeit des Kohlenstoff-11 von 20,3 Minuten limitiert seinen Nutzen. Daher ist die 18F-Fluoralkylierung eine Möglichkeit, Fluor-18, das eine Halbwertszeit von 109,8 Minuten hat, in Target-Moleküle einzuführen. Während die 18F-Fluorethylierung eine weitverbreitete Markierungsstrategie ist, wird die 18F-Fluormethylierung bisher nur selten angewendet. Eine Ursache dafür ist die geringe Stabilität der 18F-Fluormethylgruppe in vivo. Durch Substitution des Wasserstoffs in der 18F-Fluormethylgruppe durch Deuterium kann deren Stabilität jedoch deutlich erhöht werden. Dadurch kann die 18F-Fluormethylierung eine wichtige Synthesestrategie für ZNS-Liganden sein, bei denen große strukturelle Varianz zum Einführen des Fluor-18 nicht möglich ist. rnAls prosthetische Gruppen zur 18F-Fluormethylierung wurden [18F]Fluormethyltosylat und [18F]Fluor-[d2]methyltosylat mit radiochemischen Ausbeuten bis zu 50% synthetisiert. Die Reaktionsbedingungen der 18F-Fluormethylierung mit d2-[18F]FMT und die Abtrennung der Radioliganden wurden an einer Modellverbindungen und den drei Zielstrukturen [18F]Fluor-[d2]methylharmol, [18F]Fluor-[d2]methyl-MH.MZ und [18F]Fluor-[d2]methylflumazenil optimiert. Es konnten radiochemischen Ausbeuten zwischen 25 und 60% erzielt werden. rnMit allen drei ZNS-Liganden wurden Kleintier-PET-Studien durchgeführt. Das d2-[18F]FMH zeigte eine schnelle und 1,5fach höhere Anreicherung im Hirn innerhalb der ersten fünf Minuten als die Vergleichssubstanz [18F]FEH. Für d2-[18F]FM-MH.MZ wurde in vivo eine höhere spezifische Anreicherung des Radiotracers im frontalen Cortex beobachtet als bei der 18F-fluorethylierten Vergleichssubstanz. Für das [18F]Fluor-[d2]methylflumazenil konnte keine Aufnahme ins Hirn festgestellt werden, sondern es kam zur vollständigen Zersetzung des Radioliganden durch Defluorierung. d2-[18F]FMH und d2-[18F]FM-MH.MZ waren bei physiologischen Bedingungen zu mehr als 90% stabil.rn