In this study polycrystalline NiAl has been subjected to torsion deformation. Torsion has been used because of its characteristics. By this deformation mode high shear strains (gamma = 18 in this study) can be imposed on the sample. The deformation conditions are well-defined because of the local deformation mode, which is simple shear. Due to the monoclinic sample symmetry one half of the pole figure is needed in order to obtain the complete texture information, which is more than is needed e.g. by extrusion or rolling. Therefore, texture analysis might be more sensitive with respect to texture components. Furthermore, torsion deformation is characterized by being inhomogeneous in terms of the amount of shear strain and shear strain rate along the sample radius. The shear strain gradient makes the analysis of different stages of deformation on the same sample (i.e. under the same deformation conditions) possible. Another characteristic being special for torsion is that samples change their length, although no axial stress is applied. This effect is known as Swift effect and will be analyzed in detail. The deformation, microstructure and texture development subject to the shear strain are studied by different techniques (Electron Back-Scatter and High Energy Synchrotron Radiation). Beside the development of microstructure and texture with shear strain, the effect of an initial texture as well as the deformation temperature on the development of texture and microstructure constitute an important part of this study. Therefore, samples with three different initial textures were deformed in the temperature range T = 700K – 1300K. The development of the microstructure is characterized by two different regimes depending on the deformation temperature T. For T up to 1000K, continuous dynamic recrystallization (CDRX) takes place. This mechanism leads to the deformation-induced dislocations forming low angle grain boundaries (LAGBs) or being incorporated into them and the successive transformation of these boundaries into high angle grain boundaries (HAGBs) by a further increase of their misorientation. The predictions of this model were compared with the experimental results. The shear stress – shear strain curves are characterized by a peak at low strains, which is followed by softening and a steady state at high strains. This condition is fulfilled for a number of samples, but especially <111> oriented samples do not show a softening stage at low temperatures. Grain refinement takes place for all samples and the average grain size decreases with temperature. The predicted LAGB decrease is in best agreement with the experiments at the lowest temperatures (T = 700K and 800K). Deviations from the model can be explained by the temperature dependence of the grain boundary mobility. For temperatures T > 1000K, discontinuous dynamic recrystallization (DDRX) occurs, by which new grains form by nucleation and subsequent growth. The texture is characterized by two components, {100}<100> (cube, C) and {110}<100> (Goss, G). The intensity of G increases with temperature, while that of C decreases independent of the initial orientation. Both components have their maximum deviated about the 1 axis. The deviation is larger for grains containing the C component and decreases with temperature. Grains containing the G component have the smaller deviation, which decreases with temperature and strain. Texture simulations based on the full constraint Taylor model under the assumption of {110}<100> and {110}<110> slip were done with the experimental <110> and <111> fibres as well as a theoretical <100> fibre and a {100}<100> single orientation (ideal as well as rotated about the torsion axis). The G component is predicted by the simulations and is therefore a deformation texture. However the C component does not appear in the simulation. It therefore must originate by different mechanisms. For the non-<100> oriented samples, possibly nucleation is responsible for the formation of C oriented nuclei. Simulations with single orientations lead to the conclusion, that the ideal C orientation rotates about the 1 axis, while other C orientations, which are rotated about the torsion axis, increasingly converge towards the G component with strain. A single G orientation on the other hand is stable against such a rotation and is therefore the most likely steady state texture. Based on these results it is proposed, that ideally C oriented nuclei rotate until an orientation is reached into which they grow. These new grains are further rotated up to a critical angle, at which a part of them disappears either by adjacent grains or new C oriented nuclei. The recrystallization texture for T > 1000K is most likely the C component as well. Torsional creep of NiAl is characterized by a stress exponent, which depends on temperature and an activation energy, which is stress dependent. A model incorporating both dependencies is proposed and applied to the creep data. It is shown that these equations are able to describe the experimental findings. Thus creep of NiAl based on this model is dominated by non-diffusional processes such as cross slip of <100> screw dislocations for T  1000K. For T > 1000K the stress exponent and the activation energy are in a region, which according to previous reports is rather dominated by dislocation-climb controlled creep. The Swift effect, due to which samples change their axial dimension during torsion without applied axial stress, is observed for NiAl. It is strongly related to the texture development and in the case of NiAl the C component is identified as being responsible for shortening, whereas the G component leads to lengthening as long as it is not aligned with the shear system. Both tendencies can be explained based on the active slip systems. Simulations fail to predict the experimental observation, because the C component is not present. HESR and EBSD were compared with respect to local texture measurements. It was concluded depending on the average grain size HESR has an advantage in terms of grain statistics. For DDRX samples however, both methods are limited. Local texture inhomogeneities can be better detected using EBSD, whereas for an overall local texture information HESR is better suited.

In this study polycrystalline NiAl has been subjected to torsion deformation. Torsion has been used because of its characteristics. By this deformation mode high shear strains (gamma = 18 in this study) can be imposed on the sample. The deformation conditions are well-defined because of the local deformation mode, which is simple shear. Due to the monoclinic sample symmetry one half of the pole figure is needed in order to obtain the complete texture information, which is more than is needed e.g. by extrusion or rolling. Therefore, texture analysis might be more sensitive with respect to texture components. Furthermore, torsion deformation is characterized by being inhomogeneous in terms of the amount of shear strain and shear strain rate along the sample radius. The shear strain gradient makes the analysis of different stages of deformation on the same sample (i.e. under the same deformation conditions) possible. Another characteristic being special for torsion is that samples change their length, although no axial stress is applied. This effect is known as Swift effect and will be analyzed in detail. The deformation, microstructure and texture development subject to the shear strain are studied by different techniques (Electron Back-Scatter and High Energy Synchrotron Radiation). Beside the development of microstructure and texture with shear strain, the effect of an initial texture as well as the deformation temperature on the development of texture and microstructure constitute an important part of this study. Therefore, samples with three different initial textures were deformed in the temperature range T = 700K – 1300K. The development of the microstructure is characterized by two different regimes depending on the deformation temperature T. For T up to 1000K, continuous dynamic recrystallization (CDRX) takes place. This mechanism leads to the deformation-induced dislocations forming low angle grain boundaries (LAGBs) or being incorporated into them and the successive transformation of these boundaries into high angle grain boundaries (HAGBs) by a further increase of their misorientation. The predictions of this model were compared with the experimental results. The shear stress – shear strain curves are characterized by a peak at low strains, which is followed by softening and a steady state at high strains. This condition is fulfilled for a number of samples, but especially <111> oriented samples do not show a softening stage at low temperatures. Grain refinement takes place for all samples and the average grain size decreases with temperature. The predicted LAGB decrease is in best agreement with the experiments at the lowest temperatures (T = 700K and 800K). Deviations from the model can be explained by the temperature dependence of the grain boundary mobility. For temperatures T > 1000K, discontinuous dynamic recrystallization (DDRX) occurs, by which new grains form by nucleation and subsequent growth. The texture is characterized by two components, {100}<100> (cube, C) and {110}<100> (Goss, G). The intensity of G increases with temperature, while that of C decreases independent of the initial orientation. Both components have their maximum deviated about the 1 axis. The deviation is larger for grains containing the C component and decreases with temperature. Grains containing the G component have the smaller deviation, which decreases with temperature and strain. Texture simulations based on the full constraint Taylor model under the assumption of {110}<100> and {110}<110> slip were done with the experimental <110> and <111> fibres as well as a theoretical <100> fibre and a {100}<100> single orientation (ideal as well as rotated about the torsion axis). The G component is predicted by the simulations and is therefore a deformation texture. However the C component does not appear in the simulation. It therefore must originate by different mechanisms. For the non-<100> oriented samples, possibly nucleation is responsible for the formation of C oriented nuclei. Simulations with single orientations lead to the conclusion, that the ideal C orientation rotates about the 1 axis, while other C orientations, which are rotated about the torsion axis, increasingly converge towards the G component with strain. A single G orientation on the other hand is stable against such a rotation and is therefore the most likely steady state texture. Based on these results it is proposed, that ideally C oriented nuclei rotate until an orientation is reached into which they grow. These new grains are further rotated up to a critical angle, at which a part of them disappears either by adjacent grains or new C oriented nuclei. The recrystallization texture for T > 1000K is most likely the C component as well. Torsional creep of NiAl is characterized by a stress exponent, which depends on temperature and an activation energy, which is stress dependent. A model incorporating both dependencies is proposed and applied to the creep data. It is shown that these equations are able to describe the experimental findings. Thus creep of NiAl based on this model is dominated by non-diffusional processes such as cross slip of <100> screw dislocations for T  1000K. For T > 1000K the stress exponent and the activation energy are in a region, which according to previous reports is rather dominated by dislocation-climb controlled creep. The Swift effect, due to which samples change their axial dimension during torsion without applied axial stress, is observed for NiAl. It is strongly related to the texture development and in the case of NiAl the C component is identified as being responsible for shortening, whereas the G component leads to lengthening as long as it is not aligned with the shear system. Both tendencies can be explained based on the active slip systems. Simulations fail to predict the experimental observation, because the C component is not present. HESR and EBSD were compared with respect to local texture measurements. It was concluded depending on the average grain size HESR has an advantage in terms of grain statistics. For DDRX samples however, both methods are limited. Local texture inhomogeneities can be better detected using EBSD, whereas for an overall local texture information HESR is better suited.

Auf dem Weg der Bildung von Cu2Se aus den Elementen wurden die während der Reaktion auftretenden Zwischenprodukte bestimmt. Dabei wurde eine Mischung aus Kupfer- und Selenpulver in einer Kugelmühle gemahlen. Nach bestimmten Zeitintervallen wurden dem Mahlgut Proben entnommen und röntgenographisch ihre Zusammensetzung bestimmt. Zusätzlich wurden diese Proben nach dem Mahlen in der DTA gemessen. Um den Einfluss der Korngröße des Kupferpulvers zu untersuchen, wurde eine Mischung mit feinerem Kupferpulver in gleicher Weise untersucht. Es wurden 43 Glasproben der Zusammensetzung Fe2GexSe98-x, Fe4GexSe96-x und Fe6GexSe94-x hergestellt. Diese Proben wurden röntgenographisch und thermoanalytisch untersucht. Man bestimmte die Dichten, die Rekristallisationstemperaturen, die Glasübergangtemperaturen und die Schmelzpunkte jeder Probe. Die bei der Rekristallisation entstandenen Substanzen wurden über Röntgenheizkameraaufnahmen ermittelt. Aus den thermoanalytischen Daten berechnete man die Kristallinität nach Hruby. Darüber hinaus ermittelte man die kinetischen Daten der Rekristallisation. Im ternären Phasendiagramm Fe-Ge-Se wurden die Gleichgewichte zwischen den binären und ternären Verbindungen aufgestellt. Darüber hinaus klärte man die Phasenverhältnisse innerhalb der Schnitte Fe0,615Ge0,385-delta-Fe(1-x)Se und GeSe2-delta-Fe(1-x)Se auf.

In numerous Gram-negative and Gram-positive bacteria as well as in Archaea SL proteins form the outermost layer of the cell envelope. SL (glyco)monomers self-assemble with oblique (p2), tetragonal (p4), or hexagonal (p3, p6) symmetries [12]. SL subunits interact with each other and with the underlying cell surface by relatively weak non-covalent forces such as hydrogen-bonds, ionic bonds, salt-bridges or hydrophobic interactions. This makes them easy to isolate by applying chaotropic agents like urea and guanidine hydrochloride (GuHCl), chelating chemicals, or by changing the pH of the environment [10]. Upon dialysis in an ambient buffer monomers recrystallize into regular arrays that possess the forms of flat sheets, open ended cylinders, or spheres on solid substrates, at air-water intefaces and on lipid films, making them appealing for nanobiotechnological applications [3, 18]. The aim of this study was to investigate the structure, thermal stability, in vivo self-assembly process, recrystallization and metallization of three different recombinant SL proteins (SslA-eGFP, mSbsC-eGFP and S13240-eGFP) expressed in yeast S. cerevisiae BY4741 which could be further used in nanobiotechnological applications. In order to fulfill this aim, I investigated the in vivo expression of SL proteins (SslA, SbsC, S13240) tagged with eGFP (SL-eGFP) in the yeast S. cerevisiae BY4141. First, I characterized the heterologous expression of SL fusion constructs with growth and fluorescence measurements combined with Western blot analyses. Fluorescence microscopy investigations of overnight grown cultures showed that SslA-eGFP fusion protein was expressed as fluorescent patches, mSbsC-eGFP as tubular networks, and S13240-eGFP as hollow-like fibrillar network structures, while eGFP did not show any distinct structure Thermal stability of in vivo expressed SL-eGFP fusion proteins were investigated by fluorescence microscopy and immunodetection. In vivo self-assembly kinetics during mitosis and meiosis was the second main issue. In parallel, association of in vivo mSbsC-eGFP structures with the cellular components was of interest. A network of tubular structures in the cytosol of the transformed yeast cells that did not colocalize with microtubules or the actin cytoskeleton was observed. Time-resolved analysis of the formation of these structures during vegetative growth and sporulation was investigated by live fluorescence microscopy. While in meiosis ascospores seemed to receive assembled structures from the diploid cells, during mitosis surface layer structures were formed de novo in the buds. Surface layer assembly always started with the appearance of a dot-like structure in the cytoplasm, suggesting a single nucleation point. In order to get these in vivo SL assemblies stably outside the cells (in situ), cell distruption experiments were conducted. The tubular structures formed by the protein in vivo were retained upon bursting the cells by osmotic shock; however their average length was decreased. During dialysis, monomers obtained by treatment with chaotropic agents recrystallized again to form tube-like structures. This process was strictly dependent on calcium ions, with an optimal concentration of 10 mM. Further increase of the Ca2+ concentration resulted in multiple non-productive nucleation points. It was further shown that the lengths of the S-layer assemblies increased with time and could be controlled by pH. After 48 hours the average length at pH 9.0 was 4.13 µm compared to 2.69 µm at pH 5.5. Successful chemical deposition of platinum indicates the potential of recrystallized mSbsC-eGFP structures for nanobiotechnological applications. For example, such metalized protein nanotubes could be used in conductive nanocircuit technologies as nanowires.

The purpose of this report is to evaluate the hardness and microstructure in bent and welded samples of Alloy 718. The results will be used by GKN aerospace to evaluate the simulated values of the production process of vines in a jet engine. In total, eleven samples from three different production chains are evaluated. All samples are bent and go through different stages within the production including bending, solution treatment and welding. The samples are cut and mounted in bakelite then polished and etched in order for the microstructure to be seen and evaluated. Hardness tests were made on the mounts to evaluate how bending, solution treatment and welding affects the hardness. The bent samples without the solution treatment became harder depending on the amount of cold deformation. The amount of cold deformation controls how fast the material recrystallizes during subsequent solution treatment. During the solution treatment, the δ-phase (Ni3Nb) is precipitated in the grain boundaries which prevents a coarser grain size and therefore promotes a smaller grain size.  The laser weld creates a small HAZ (heat affected zone) that becomes softer because the heat dissolves the δ-phase which therefore triggers the grains to grow. The weld consists of eutectic γ-dendrites with interdendritic pools of alloying elements. After the solution treatment, many needle shaped δ-phases arise from the pools and HAZ. The hardness measurements were tested on a manual machine which makes potential human error important to consider when the measurements are evaluated. When the grain size measurements are done on the solution treated samples, the grain boundaries can be difficult to determine because the δ-phases and twins create wide and incorrect boundaries. The results will be used by GKN Aerospace in order to verify their simulations. The heterogenic material after solution treatment will probably be studied further. / Syftet med projektet är att undersöka hårdhet och mikrostruktur i bockade och svetsade prover tillverkade av Alloy 718. Totalt undersöks elva stycken prover som är tillverkade på olika sätt enligt tre tillverkningskedjor. Alla provbitar är bockade och har sedan genomgått olika många steg i tillverkningen som består utav bockning, upplösningsbehandling och svets. Genom att kapa upp provbitarna i mindre bitar, baka in de i bakelit och etsa de studerades mikrostrukturen och hur den påverkas av bockning, upplösningsbehandling och svets. Vidare gjordes hårdhetsmätningar över olika delar av proven för att undersöka hur mycket hårdare materialet blir vid kalldeformation och hur upplösningsbehandling och svets påverkar hårdheten i Alloy 718. Endast bockade prov blir hårdare beroende på hur mycket kalldeformation provbiten har utsatts för. Hur mycket provet har deformerats styr hur snabbt rekristallisationen sker vid en efterföljande upplösningsbehandling. Under upplösningsbehandlingen utskiljs även δ-fas (Ni3Nb) i korngränser vilket främjar en mindre kornstorlek. Lasersvetsen ger ett litet värmepåverkat område men värmen från svetsen bidrar till att δ-fasen löses upp och större korn bildas. Svetsen består av långa eutektiska γ-dendriter med interdendritiska poler av mycket legeringsämnen. Vid upplösningsbehandling efter utförd svets bildas det δ-fas i de värmepåverkade och i svetsen. Hårdhetsmätningarna har utförts på en manuell hårdhetsmaskin vilket innebär att felmarginalen blir större då den mänskliga felfaktorn spelar en stor roll. Vid beräkning av kornstorlek har det varit svårt att utskilja vad som är en korngräns i upplösningsbehandlade prov då mängden δ-fas efter upplösningsbehandling ger tjocka korngränser.  Resultaten kommer användas av GKN Aerospace för att verifiera sina simulationer. Det heterogena materialet efter upplösningsbehandlingen kommer troligtvis studeras vidare.

In numerous Gram-negative and Gram-positive bacteria as well as in Archaea SL proteins form the outermost layer of the cell envelope. SL (glyco)monomers self-assemble with oblique (p2), tetragonal (p4), or hexagonal (p3, p6) symmetries [12]. SL subunits interact with each other and with the underlying cell surface by relatively weak non-covalent forces such as hydrogen-bonds, ionic bonds, salt-bridges or hydrophobic interactions. This makes them easy to isolate by applying chaotropic agents like urea and guanidine hydrochloride (GuHCl), chelating chemicals, or by changing the pH of the environment [10]. Upon dialysis in an ambient buffer monomers recrystallize into regular arrays that possess the forms of flat sheets, open ended cylinders, or spheres on solid substrates, at air-water intefaces and on lipid films, making them appealing for nanobiotechnological applications [3, 18]. The aim of this study was to investigate the structure, thermal stability, in vivo self-assembly process, recrystallization and metallization of three different recombinant SL proteins (SslA-eGFP, mSbsC-eGFP and S13240-eGFP) expressed in yeast S. cerevisiae BY4741 which could be further used in nanobiotechnological applications. In order to fulfill this aim, I investigated the in vivo expression of SL proteins (SslA, SbsC, S13240) tagged with eGFP (SL-eGFP) in the yeast S. cerevisiae BY4141. First, I characterized the heterologous expression of SL fusion constructs with growth and fluorescence measurements combined with Western blot analyses. Fluorescence microscopy investigations of overnight grown cultures showed that SslA-eGFP fusion protein was expressed as fluorescent patches, mSbsC-eGFP as tubular networks, and S13240-eGFP as hollow-like fibrillar network structures, while eGFP did not show any distinct structure Thermal stability of in vivo expressed SL-eGFP fusion proteins were investigated by fluorescence microscopy and immunodetection. In vivo self-assembly kinetics during mitosis and meiosis was the second main issue. In parallel, association of in vivo mSbsC-eGFP structures with the cellular components was of interest. A network of tubular structures in the cytosol of the transformed yeast cells that did not colocalize with microtubules or the actin cytoskeleton was observed. Time-resolved analysis of the formation of these structures during vegetative growth and sporulation was investigated by live fluorescence microscopy. While in meiosis ascospores seemed to receive assembled structures from the diploid cells, during mitosis surface layer structures were formed de novo in the buds. Surface layer assembly always started with the appearance of a dot-like structure in the cytoplasm, suggesting a single nucleation point. In order to get these in vivo SL assemblies stably outside the cells (in situ), cell distruption experiments were conducted. The tubular structures formed by the protein in vivo were retained upon bursting the cells by osmotic shock; however their average length was decreased. During dialysis, monomers obtained by treatment with chaotropic agents recrystallized again to form tube-like structures. This process was strictly dependent on calcium ions, with an optimal concentration of 10 mM. Further increase of the Ca2+ concentration resulted in multiple non-productive nucleation points. It was further shown that the lengths of the S-layer assemblies increased with time and could be controlled by pH. After 48 hours the average length at pH 9.0 was 4.13 µm compared to 2.69 µm at pH 5.5. Successful chemical deposition of platinum indicates the potential of recrystallized mSbsC-eGFP structures for nanobiotechnological applications. For example, such metalized protein nanotubes could be used in conductive nanocircuit technologies as nanowires.

Bakterielle Zellhüllenproteine (S-Schichten) können als molekulare Bausteine zur Funktionalisierung technischer Oberflächen verwendet werden. Die Proteine fungieren dabei als formgebende Muster (Template) oder vermitteln Bindungsstellen für eine nanostrukturierte Materialsynthese. In der vorliegenden Arbeit werden drei S-Schicht-Varianten elektronenmikroskopisch und kraftmikroskopisch charakterisiert und deren Templateigenschaften für die nasschemische Platin- und Goldclusterabscheidung vorgestellt. Für die Metallisierbarkeit der S-Schichten werden unterschiedliche Wege beschrieben. So wird unter anderem eine neue Methode zur Negativkontrastierung der kristallinen S Schichten für die Transmissionselektronenmikroskopie vorgestellt. Dabei werden adsorbierte und mit Metallkomplexen aktivierte S-Schichten kurzzeitig einer UV-Strahlung ausgesetzt. Verschiedene Methoden für die Beschichtung von technischen Oberflächen mit S Schichtproteinen werden aufgezeigt, insbesondere die Entwicklung einer neuen Technik für die Beschichtung von vorstrukturierten Sensoroberflächen, für die mikrofluidische Reaktionsräume geschaffen werden. Durch optimierte Reaktionsbedingungen wird unter Nutzung des Selbstorganisationsvermögens der Proteinmonomere eine großflächige Beschichtung von Substratoberflächen erreicht. Dies führt bei Anwendung der direkten Rekristallisation des Proteins an der Substratoberfläche zur Ausbildung von Monolagen. Untersuchungen zur Stabilisierung der S-Schichten am Substrat zeigen, dass diese durch den Einsatz von proteinvernetzenden Substanzen, wie Glutaraldehyd, erhöht werden kann. Weiterhin wird eine bionanotechnologische Funktionalisierung von mikroelektronischen Sensorstrukturen durch Integration metallisierter S-Schichtproteine ausführlich beschrieben. Erste Messergebnisse mit einem funktionalisierten Pyrosensor zeigen eine bessere Sensitivität durch die Erhöhung der katalytischen Aktivität an der Oberfläche der Nanocluster. Die Beschichtung und Vermessung neu entwickelter Piezosensoren der Siemens AG zeigt die hohe Sensitivität dieser Sensoren. Die dynamischen Messungen der Massenänderung während des Rekristallisationsprozesses werden durch ein theoretisches Modell zur Proteindeposition aus einer Monomerlösung interpretiert. Abstract* Bacterial surface layer proteins (S-layer proteins) can be used as molecular building blocks for the functionalisation of technically-used surfaces. For example, the proteins serve as templates for the production of well-defined patterns or provide binding sites for material synthesis at nanoscale. In this thesis, three different S-layer proteins are characterised by electron and atomic force microscopy. The properties of these proteins for being templates for the deposition of platinum and gold clusters are introduced. Different ways for the metallisation of S-layers are described. One example for this is a new method of negative staining of crystallised S-layers for the transmission electron microscopy, where the S-layers, adsorbed and activated with metal complexes, are exposed to UV for a short time. Different methods for coating technically-used surfaces are presented, especially a new technique for coating structured sensors' surfaces, which uses microfluidic reaction areas. The coating of large substrate surfaces with protein monomers is achieved by controlling the reaction conditions of the self-assembly process. If discrete recrystallisation takes place on the surface, the process leads to the formation of protein monolayers. Investigations showed that the stabilisation of the S-layers on a substrate can be increased by adding protein-linking reagents (e.g. glutaraldehyde). Furthermore, a bionanotechnological functionalisation of microelectronic sensors' surfaces by integrating metalised S-layer proteins is described in detail. First results show an increased catalytic activity on the surfaces of the nanoclusters. The coating of sensor surfaces with S-layers has recently been used to develop a piezoelectric sensor by the Siemens AG. This novel sensor has shown high sensitivity. Dynamic measurements of mass change during the recrystallisation process are described by a theoretical model for protein deposition out of a monomer solution.

Die vorliegende Arbeit behandelt die Wechselwirkung von Verarbeitung und Gefüge Mn-Al basierter hartmagnetischer Werkstoffe sowie die Auswirkung des Gefüges auf deren Eigenschaften. Dabei wurde das Gefüge der metastabilen tau-Phase im Anschluss an die Phasenbildung aus der Hochtemperaturphase epsilon-MnAl und die Auswirkung einer anschließenden Umformung untersucht. Der Schwerpunkt der Arbeit lag in der Analyse der Evolution verschiedener Gefügebestandteile, wie Grenzflächenverteilung, Versetzungen und Korngröße unter Verwendung von Rasterelektronenmikroskopie und Elektronenrückstreubeugung. Die epsilon-tau Umwandlung kann auf 2 verschiedene Routen erfolgen. In beiden Fällen wird die Bildung von 3 kristallographisch unterschiedlichen zwillingsähnlichen Defekten beobachtet, die als wahre Zwillinge, Ordnungszwillinge und Pseudozwillinge bezeichnet werden. Sie lassen sich als Rotationen um einen kristallographischen {111}-Pol beschreiben. Der Anteil der Zwillingsdefekte nach der Umwandlung, aber auch die Korngröße und Versetzungsdichte sind von der gewählten Umwandlungsroute abhängig. Während die Sättigungspolarisation annähernd gleich ist, reagiert die Koerzitivfeldstärke sensitiv auf den Gefügezustand. Eine niedrige Korngröße und hohe Versetzungsdichte tragen zu ihrer Erhöhung bei. Eine anschließende Kaltumformung erzeugt ein vielfach verzwillingtes Verformungsgefüge mit hoher Koerzitivfeldstärke. Wärmebehandlungen und die Analyse der Schärfe von Kikuchi-Beugungsbildern haben gezeigt, dass nicht die hohe Zwillingsdichte, sondern primär Versetzungen im Verformungsgefüge die Koerzitivfeldstärke steigern. Warmumformung von tau-MnAl führt zur dynamischen Rekristallisation. Die Kinetik der Gefügeneubildung und die resultierende Korngröße sind stark von der Umformtemperatur abhängig. Durch Umformung lässt sich eine kristallographische Texturierung von tau-MnAl erreichen. Die Orientierung der magnetisch leichten [001]-Richtung ist dabei vom gewählten Umformverfahren und gegebenenfalls von der Nachbehandlung abhängig. Statische und dynamische Rekristallisation reduzieren den Anteil der Zwillingsdefekte signifikant und besonders Pseudozwillinge und Ordnungszwillinge werden im Gefüge beseitigt. Das Rekristallisationsgefüge weist gegenüber dem Umwandlungsgefüge einen geringeren Widerstand gegen die mit der Zersetzungsreaktion verbundene Bildung von beta-Mn auf. Die Ursache liegt in einer selektiven beta-Mn-Bildung an allgemeinen Korngrenzen, während die Zwillingsdefekte einen erhöhten Widerstand gegen sie Zersetzung aufweisen.

Im Rahmen der vorliegenden Arbeit wurde eine Warmwalztechnologie für gießgewalztes Vorband der calciumhaltigen Magnesiumlegierung Mg-2Zn-1Al-0,3Ca (ZAX210) entwickelt. Ausgangspunkt war die Untersuchung des Verformungs- und Rekristallisationsverhaltens in Abhängigkeit der Umformtemperatur, Umformgeschwindigkeit und des Umformgrades. Dabei wurde die zwillingsinduzierte dynamische Rekristallisation als dominierender Rekristallisationsmechanismus vor allem bei erhöhten Umformgeschwindigkeiten identifiziert. Basierend auf den daraus gewonnenen Erkenntnissen konnte ein Prozessfenster für das Warmwalzen abgeleitet werden, welches die Erzeugung eines 2 mm dicken Fertigbandes mit abgeschwächter Textur, guten mechanischen Eigenschaften und einer verbesserten Umformbarkeit, insbesondere im Vergleich zu den Standardknetlegierungen AZ31 und ZE10, erlaubte. Die Warmwalzparameter sind unter Berücksichtigung gleicher Randbedingungen auf einen industriellen Warmwalzprozess übertragbar.

The late Variscan rapid extrusion of ultra-high pressure metamorphic rocks into a preexisting nappe stack is the striking feature of the Erzgebirge, N-Bohemian Massif. Complex deformation increments, the large scatter of orientation and geometry of the finite strain ellipsoid as well as partly inverted metamorphic and age profiles are controversially discussed. Structural analysis and geothermobarometry show that deeply buried continental crust emplaced under transpression with horizontal σ1 (NNW-SSE) and σ3 stress axes. Thereby, west-directed lateral escape of isothermally exhumed high-pressure units led to the formation of an exhumation channel. The pervasive fabric of quartz-feldspar rocks formed between 400–650 °C. Based on Ar-Ar geochronology, the deformation in the exhumation channel is framed between 340 and 335 Ma. This preliminary results allow a modern texture analysis of natural shear zones, i.e. electron back scattering and neutron diffraction of quartz from shear zones of the exhumation channel. Because of an extensive and complex dataset, the crystallographic orientation of quartz is statistically analysed. I applied multidimensional scaling of the error between orientation density functions to visualize quartz textures together with additional microstructural features. I show that the temporal coexistence of two crystallographic orientation endmembers is the exclusive result of varying strain rates and differential stress. This thesis combines for the first time crystallographic textures of the Erzgebirge with modern plate tectonic concepts of the European Variscan orogeny.:Table of contents PREFACE Channel exhumation models in collisional Orogens Texture evolution of quartz in orogenic shear zones The structure of the thesis PART 1: THE EXHUMATION CHANNEL OF THE ERZGEBIRGE: GEOLOGICAL CONSTRAINS 1 Introduction 2 Geological Setting 2.1 The Variscan orogeny 2.2 The Saxo-Thuringian Zone as part of the European Variscides 2.3 Tectonics – constraints for an exhumation channel (<340 Ma) 3 Methods and Data processing 3.1 Field work, sample collection and selection 3.2 Geochemistry 3.3 MLA 3.4 EMP analyses and pressure-temperature estimations 3.5 Ar-Ar dating 3.6 Ar-Ar data handling and statistical treatment 4 Results 4.1 Geochemistry and Mineral Content of the Channel Rocks 4.2 Tectonics of the exhumation channel 4.2.1 Mica schists – roof of the channel 4.2.2 Paragneisses and Orthogneiss (type 1) 4.2.3 Orthogneiss (mgn) 4.2.4 Orthogneiss (type 2) – footwall of the channel 4.3 Petrology and Mineral chemistry 4.3.1 Garnet 4.3.2 Plagioclase 4.3.3 White mica 4.3.4 Biotite 4.4 Geothermobarometry 4.5 40Ar/39Ar – geochronology 4.5.1 Step heating 4.5.2 Single grain fusion 4.5.3 Ar-Ar and mineral chemistry 4.5.4 Ar-Ar and structural geology 5 The tectonometamorphic evolution of the exhumation channel 5.1 Local change in finite strain ellipsoid orientation 5.2 Evidence for advective heat transfer during exhumation 5.3 Position of the gneiss complex Reitzenhain-Catherine 5.4 Do Ar-Ar ages of the Erzgebirge represent cooling or recrystallization? 6 The channel model 6.1 Pre-channel stage – subduction 6.2 Channel stage – lateral extrusion 6.3 Post-channel stage – extensional doming 7 The Constrains for Texture analyses in a channel-type exhumation shear zone PART 2: QUARTZ TEXTURE AND MICROSTRUCTURAL EVOLUTION IN A CHANNEL-TYPE EXHUMATION SHEAR ZONE 1 Introduction 2 State of the Art 2.1 Dynamic recrystallization mechanism in quartz. 2.2 Texture evolution from natural and experimental deformed quartz 2.3 Quartz c-axis and textures in the Erzgebirge 3 Sample description 3.1 Mineral content 3.2 Quartz microstructures 3.2.1 Type 1 – Predominance of GBM 3.2.2 Type 2 – GBM overprints SGR 3.2.3 Type 3 – Equal ratio of GBM and SGR 3.2.4 Type 4 – Predominance of SGR 4 Methods 4.1 Time of Flight data processing and analysis 4.2 EBSD data processing and analysis 4.3 Multidimensional scaling 5 Results 5.1 Pole figure geometry 5.2 Multidimensional scaling 5.3 Texture properties and recrystallization 5.4 Grain and sample properties 5.5 Intragranular misorientation 5.6 Subgrain misorientation axes, slip systems and Schmid factor 6 Discussion 6.1 The dependence of quartz content and distribution and the particular CPO 6.2 The context between grain sizes, shape preferred orientation (SPO) and crystal preferred orientation (CPO) 6.3 Active slip systems during ductile quartz deformation 6.4 Recrystallization mechanism and texture 7 Conclusions GENERAL CONCLUSIONS REFERENCES APPENDIX A Isochemistry during metamorphism B Confidentiality of the PT estimations C Discrepancy of WPA and WMA D Appendix Figures E Appendix Tables