The main focus of the present work was the Ge-rich part of the binary Ba – Ge system, in which by inspecting the behavior of the clathrate-I Ba8Ge43 under pressure, several new phases were found. The new phases in this system have the following compositions: BaGe3 (with two modifications), BaGe5, BaGe5.5 and BaGe6, therefore they are quite close in composition range: 75% - ~85% at. Ge. Concerning the conditions required for the synthesis of each phase, several combinations of temperature and pressure were employed in order to find a stability range. It was possible to establish such a formation range for all phases. In some cases two phases were found for a given conditions and in many other cases three or more phases were found to coexist. Thus, the stability range of pressure and temperature for single phase formation turned out to be very narrow. By inspecting of some structural features, for instance the interatomic distances, it is found that the average of the Ge – Ge distances change in line with the composition, i.e. the shorter contacts belong to BaGe6 while the longer distances are present in BaGe3 (both modification). An opposite trend is observed for the calculated density of each phase (neglecting the tI32 form of BaGe3): the lower density is found for BaGe3 and the denser compound is found to be BaGe6. Of course this is not coincidence, since due to the Ge content, BaGe6 has the largest molar mass. Similarly, by examining the density as a function of the interatomic distance. In such case, the denser compound is characterized by shorter Ge – Ge contacts, while the less dense phase holds the longest Ge – Ge contacts. This is in agreement with the building motifs within each crystal structure: columns in BaGe3 (open framework) passing through layers in BaGe5, ending in a three-dimensional network (closed framework) in BaGe6.

The main focus of the present work was the Ge-rich part of the binary Ba – Ge system, in which by inspecting the behavior of the clathrate-I Ba8Ge43 under pressure, several new phases were found. The new phases in this system have the following compositions: BaGe3 (with two modifications), BaGe5, BaGe5.5 and BaGe6, therefore they are quite close in composition range: 75% - ~85% at. Ge. Concerning the conditions required for the synthesis of each phase, several combinations of temperature and pressure were employed in order to find a stability range. It was possible to establish such a formation range for all phases. In some cases two phases were found for a given conditions and in many other cases three or more phases were found to coexist. Thus, the stability range of pressure and temperature for single phase formation turned out to be very narrow. By inspecting of some structural features, for instance the interatomic distances, it is found that the average of the Ge – Ge distances change in line with the composition, i.e. the shorter contacts belong to BaGe6 while the longer distances are present in BaGe3 (both modification). An opposite trend is observed for the calculated density of each phase (neglecting the tI32 form of BaGe3): the lower density is found for BaGe3 and the denser compound is found to be BaGe6. Of course this is not coincidence, since due to the Ge content, BaGe6 has the largest molar mass. Similarly, by examining the density as a function of the interatomic distance. In such case, the denser compound is characterized by shorter Ge – Ge contacts, while the less dense phase holds the longest Ge – Ge contacts. This is in agreement with the building motifs within each crystal structure: columns in BaGe3 (open framework) passing through layers in BaGe5, ending in a three-dimensional network (closed framework) in BaGe6.

Der Schwerpunkt der vorliegenden Arbeit lag auf der Synthese neuer binärer tetrelreicher Silicide und Germanide der Erdalkali- und Seltenerdmetalle. Die Verbindungen wurden unter Hochdruck-Hochtemperaturbedingungen mit einer Vielstempelpresse bei Drücken bis 15 GPa und Temperaturen bis 1500 K synthetisiert und umfassend charakterisiert. Im Rahmen dieser Arbeit konnten binäre Silicide und Germanide der Erdalkali- und Seltenerdmetalle, basierend auf der Analyse der auftretenden Strukturmotive, insbesondere in der anionischen Teilstruktur, und der Anzahl der homoatomaren Tetrel-Tetrel-Bindungen, klassifiziert werden. Sieben Gruppen können unterschieden werden: Strukturen mit dichtesten Packungen, isolierten Atomen und Tt2-Hanteln (und Vierecken), isolierten Polyanionen, Ketten und Bändern, Schichten und Netzwerken. Die letzte Gruppe kann weiter in die Untergruppen dreidimensionaler Netzwerke ohne unterscheidbare Polyanionen, mit unterscheidbaren Polyanionen und aus unterscheidbaren kondensierten Käfigen in der anionischen Teilstruktur eingeteilt werden. Bei den Verbindungen dieser Arbeit handelt es sich im Falle derer mit einer 1:3 Zusammensetzung um atomare Anordnungen mit kubisch dichtester Packung oder Schichtstrukturen. Die siliciumreicheren Verbindungen sind den Käfigverbindungen zuzuordnen. In den binären Systemen M-Tt (M = Ba, Sm, Lu) konnten die Tritetrele SmGe3, LuGe3 und BaSi3 erhalten werden. SmGe3 besitzt eine neue 2×2×2-Überstruktur des kubisch primitiven Cu3Au-Typs. Temperaturabhängige Messungen der magnetischen Suszeptibilität und des spezifischen elektrischen Widerstands zeigen metallisches Verhalten. LuGe3 ist isotyp zu DyGe3 und besitzt Ketten und Doppelschichten in der anionischen Ge-Teilstruktur. Messungen der magnetischen Suszeptibilität, der spezifischen Wärmekapazität und des spezifischen elektrischen Widerstands zeigen den Übergang in einen supraleitenden Zustand unterhalb einer Temperatur von 3.3(3) K. Um die Ge-Ketten mit im Vergleich zu elementaren Germanium langen Abständen dGe-Ge an Pulver- und Einkristalldaten näher zu charakterisieren, ist LuGe (FeB-Typ) mit dem Strukturmotiv eindimensionaler Germaniumketten als Referenzverbindung synthetisiert worden. Der Abstand in der eindimensionalen Germaniumkette steht in guter Übereinstimmung zu demjenigen in LuGe3 sowie zahlreicher weiterer Silicide und Germanide mit diesem Strukturmotiv. Die Bindungsanalyse der Ge-Ketten hat homoatomare Wechselwirkungen der Germaniumatome sowie heteroatomare Interaktionen unter Beteiligung von mehreren Lutetium- und Germaniumatomen ergeben. Im Falle von LuGe konnten sogar Hinweise auf Metall-Metall-Wechselwirkungen gefunden werden. Wechselwirkungen zwischen fünf Atomen konnten auch zwischen den Ge-Ketten und Lu in LuGe3 und zwischen dem jeweiligen Metallatom und den Tetrelschichten in BaSi3 bzw. -doppelschichten in LuGe3 gefunden werden. BaSi3 zeigt eine einzigartige atomare Anordnung, die als Deformationsvariante des CaGe3-Typs aufgefasst werden kann. Die Temperaturabhängigkeit des spezifischen elektrischen Widerstands und Messungen der magnetischen Suszeptibilität deuten auf metallisches Verhalten hin. In den binären Systemen Mg-Si und Sr-Si sind siliciumreiche Verbindungen mit kondensierten Käfigen in der anionischen Teilstruktur gefunden worden. Die Bestimmung der Kristallstruktur von MgSi5 mittels Elektronendiffraktion hat die Grundlage für die Phasenbestimmung im Prozess der Syntheseoptimierung gebildet, was die Synthese von für Röntgendiffraktionsexperimente geeigneten Einkristallen ermöglicht hat. Die Kristallstruktur von MgSi5 (Raumgruppe Cmme) stellt einen neuen Typ eines Netzwerks vierbindiger Siliciumatome dar, welche Si15-Käfige um die Magnesiumatome bildet. Zwei Arten kleinerer Si8-Käfige bleiben leer. Die atomaren Wechselwirkungen werden durch zwei-Zentren-Bindungen innerhalb des Siliciumnetzwerks charakterisiert. Zusätzlich gibt es Wechselwirkungen unter Beteiligung von mehreren Magnesium- und Siliciumatomen in den großen Käfigen. Die Verbindung ist diamagnetisch. Sr8Si46 ist isotyp zu Na8Si46 (Clathtrat-I). Die Charakterisierung der Struktur ist an Pulver- und Einkristalldaten durchgeführt worden. Die Bindungsanalyse zeigt neben konventionellen kovalenten Bindungen innerhalb des Siliciumnetzwerks zusätzliche Wechselwirkungen zwischen mehreren Strontium- und Siliciumatomen in den Käfigen. Physikalische Messungen belegen den Übergang in den supraleitenden Zustand bei Temperaturen unterhalb von 3.8(3) K. Bei Normaldruck zersetzen sich die Hochdruckphasen, mit Ausnahme von LuGe, exotherm in Randphasen, die im jeweiligen Phasendiagramm stabil sind, und belegen damit ihren metastabilen Charakter. Die systematische Analyse von Zusammensetzungen und Tetrelkonnektivitäten in Polyanionen binärer tetrelreicher Silicide und Germanide der Erdalkali- und Seltenerdmetalle hat eine Vielfalt von Motiven ergeben, deren Elektronenbilanz den klassischen Elektronenzählregeln nicht entspricht. Solche Grenzfälle zwischen Zintl-Phasen und intermetallischen Verbindungen können wichtige Einsichten in die chemische Bindung und Bausteine für die Entwicklung neuer Konzepte liefern. Diese Betrachtungen haben tetrelreiche Verbindungen mit der Zusammensetzung MTtx (M = Erdalkali- oder Seltenerdmetall, Tt = Si, Ge, x ≥ 3) als interessantes Arbeitsgebiet offenbart. Die Synthese dieser Verbindungen bedarf häufig Hochdruck-(Hochtemperatur)-Bedingungen. Während metallreiche Verbindungen meist dicht gepackte Strukturen aufweisen, in denen ionische Wechselwirkungen eine große Rolle spielen, wird die Bedeutung kovalenter Wechselwirkungen in tetrelreichen Verbindungen mit der Zusammensetzung MTtx (M = Erdalkali- oder Seltenerdmetall, Tt = Si, Ge, x ≥ 3) beispielsweise durch die Ähnlichkeit der normierten Volumina zu denen der entsprechenden Tetrele beleuchtet. Diese kovalenten Wechselwirkungen gehen meist mit metallischer Leitfähigkeit und in einigen Fällen mit Supraleitung einher. Zahlreiche dieser tetrelreichen Verbindungen überschreiten den Gültigkeitsbereich der 8-N-Regel und weisen keine elektronenpräzise Elektronenbilanz gemäß dem Zintl-Konzept auf. Die Untersuchung der interatomaren Abstände, Koordination und der chemischen Bindung schafft die Grundlage für die Entwicklung eines Konzepts zum Verständnis von Verbindungen, die sich an der Grenze zwischen Zintl-Phasen und intermetallischen Verbindungen befinden. Die Analyse der chemischen Bindung hat für die untersuchten Verbindungen Elektronenpaare offenbart, die in einem isolierten Molekül freien Elektronenpaaren entsprechen würden und die zu Wechselwirkungen zwischen der anionischen Partialstruktur und den Metallatomen beitragen.:Danksagung I 1. Einleitung 1 2. Grundlagen 3 2.1. Bindungskonzepte in polaren intermetallischen Phasen 3 2.1.1. Zintl-Klemm-Konzept 3 2.1.2. Quantenchemische Berechnungen zur Analyse der chemischen Bindung 4 2.2. Einfluss von Hochdruck- und Hochtemperaturbedingungen auf Materie 6 2.2.1. Hochdruck-Hochtemperaturmethoden im Überblick 8 2.2.2. Thermodynamische und kinetische Betrachtungen 10 2.2.3. Strukturelle Phasenumwandlungen unter Druck 12 2.2.4. Hochdruckmodifikationen der Tetrele 13 3. Methodik 15 3.1. Präparative Methoden 15 3.1.1. Edukte 15 3.1.2. Ausgangsverbindungen 15 3.1.3. Hochdruck-Hochtemperatur-Synthese 16 3.2. Charakterisierung 22 3.2.1. Thermische Analyse 22 3.2.2. Pulverröntgendiffraktometrie 22 3.2.3. Einkristallröntgendiffraktometrie 23 3.2.4. Chemische Analyse 23 3.2.5. Dichtebestimmung 24 3.2.6. Metallographische Analyse 24 3.2.7. Transmissionselektronenmikroskopie 25 3.2.8. Kernspinresonanzspektroskopie 26 3.2.9. Quantenchemische Berechnungen 27 3.2.10. Physikalische Eigenschaften 28 4. Ergebnisse 33 4.1. Strukturelle Klassifikation binärer Silicide und Germanide mit Erdalkaliund Seltenerdmetallen 33 4.2. SmGe3 38 4.2.1. Synthese 38 4.2.2. Charakterisierung 38 4.3. LuGe 45 4.3.1. Darstellung 45 4.3.2. Charakterisierung 45 4.4. LuGe3 51 4.4.1. Synthese 51 4.4.2. Charakterisierung 52 4.5. BaSi3 62 4.5.1. Darstellung 62 4.5.2. Charakterisierung 62 4.6. MgSi5 72 4.6.1. Synthese 72 4.6.2. Charakterisierung 73 4.7. Sr8Si46 80 4.7.1. Präparation 80 4.7.2. Charakterisierung 80 4.8. Diskussion 91 4.8.1. Dichteste Packung in SmGe3 91 4.8.2. Ketten in LuGe und LuGe3 93 4.8.3. Schichten in BaSi3 und LuGe3 94 4.8.4. Kristallchemischer Vergleich von dichtesten Packungen, isolierten Polyanionen, Ketten und Schichten in Tritetreliden 95 4.8.5. Käfigverbindungen MgSi5 und Sr8Si46 101 5. Vergleichende Diskussion binärer Silicide und Germanide der Erdalkali- und Seltenerdmetalle 105 6. Zusammenfassung 113 Literaturverzeichnis 117 Abkürzungs- und Symbolverzeichnis 153 Abbildungsverzeichnis 157 Tabellenverzeichnis 167 Publikationen 169 Lebenslauf 171 Beiträge zu dieser Arbeit 173 A. Anhang 175 A.1. Grundlagen 175 A.1.1. Hochdruckmodifikationen der Tetrele 175 A.1.2. Bekannte binäre Silicide und Germanide mit Erdalkali- und Seltenerdmetallen 175 A.2. Methodik 179 A.2.1. Edukte 179 A.3. Ergebnisse 179 A.3.1. Sm3Ge5 179 A.3.2. SmGe3 181 A.3.3. MgSi5 181 A.4. Vergleichende Diskussion der binären Silicide und Germanide dieser Arbeit 182 B. Anhang 183 B.1. Ergebnisse 183 B.1.1. SmGe3 183 B.1.2. LuGe 185 B.1.3. LuGe3 188 B.1.4. BaSi3 192 B.1.5. MgSi5 195 B.1.6. Sr8Si46 203 Eidesstattliche Erklärung 210

In dieser Dissertation wird die Darstellung tetrelreicher Seltenerdmetall–Verbindungen in den Systemen SE:Tt (SE = La, Nd, Sm, Gd, Tb, Ho, Lu; Tt = Si, Ge) und die Charakterisierung ihrer Eigenschaften beschrieben. Diese Verbindungen, welche mittels der Hochdruck–Hochtemperatur–Methode dargestellt wurden, zeigen neuartige Verknüpfungsmuster in der Tetrel–Partialstruktur. Neben der Charakterisierung der Verbindungen hinsichtlich der thermischen Stabilität und der physikalischen Eigenschaften bei Normaldruck wurde bei den Germanium–reichen Seltenerdmetall–Verbindungen eine Untersuchung der Veränderungen der Kristallstruktur bei Variation des Drucks oder der Temperatur vorgenommen. Die dargestellten Seltenerdmetall–Trisilicide SESi3 (SE = Gd, Ho, Lu) kristallisieren tetragonal isotyp zu YbSi3. LuSi3 zeigt Supraleitung mit Tc = 7.0 K. In den Systemen Gd–Si und SE–Ge (SE = La, Nd, Sm, Gd, Tb) wurden die Verbindungen GdSi5 und SEGe5 (SE = La, Nd, Sm, Gd, Tb) synthetisiert. Sie kristallisieren orthorhombisch isotyp zu LaGe5. Durch in–situ Röntgenbeugungsexperimente bei erhöhten Temperaturen kann die Existenz metastabiler Germanium–ärmerer Verbindungen SE2Ge9 (SE = Nd, Sm) nachgewiesen werden. Es handelt sich um Defektvarianten der Verbindungen SEGe5 (SE = Nd, Sm). Die strukturelle Verwandtschaft zum Aristotyp SEGe5 wird anhand einer Gruppe–Untergruppe–Beziehung aufgezeigt. Eine alternative Synthesemethode zur Darstellung tetrelreicher Verbindungen mit Gerüststrukturen bei extremen Reaktionsbedingungen stellt das Spark–Plasma–Sinterverfahren (SPS) dar. Die Darstellung der Clathratphase Ba8Ga16±xGe30∓x (x = 0, 1) erfolgte mittels SPS aus den Precursoren BaGa2±x (x = 0, 0.125) und Germanium. Die Untersuchungen der thermoelektrischen Eigenschaften zeigen, dass durch Variation der nominellen Zusammensetzung sowohl n–leitende als auch p–leitende Eigenschaften erhalten werden können. / In this thesis the synthesis of tetrel–rich rare–earth metal compounds in the systems RE:Tt (RE = La, Nd, Sm, Gd, Tb, Ho, Lu; Tt = Si, Ge) and the characterization of their properties is described. These compounds, synthesized by means of high–pressure high–temperature method, show new structural motifs in the tetrel partial structure. The compounds were characterized with respect to their thermal stability and their physical properties at ambient pressure. In addition, the changes in the crystal structure of the germanium-rich rare–earth metal compounds by variation of pressure or temperature were investigated. The synthesized rare–earth trisilicides SESi3 (SE = Gd, Ho, Lu) crystallize tetragonal, isotypic to YbSi3. LuSi3 is a superconductor with Tc = 7.0 K. In the systems Gd–Si and SE–Ge (SE = La, Nd, Sm, Gd, Tb) the compounds GdSi5 and SEGe5 (SE = La, Nd, Sm, Gd, Tb) were synthesized. They crystallize orthorhombic isotypic to LaGe5. Using in-situ high–temperature X-ray experiments the metastable germanium-poorer compounds SE2Ge9 (SE = Nd, Sm) could be observed. These compounds are defect variants of the pentagermanides SEGe5 (SE = Nd, Sm). The structural relationship to the aristotype SEGe5 is given via a group-subgroup relation. An alternative synthesis route for the preparation of tetrel–rich compounds with framework structures at extreme reaction conditions is the spark plasma sintering method (SPS). The clathrate phase Ba8Ga16±xGe30∓x (x = 0, 1) was synthesized from the precursors BaGa2±x (x = 0, 0.125) and germanium by means of SPS. The investigation of the thermoelectric properties shows, that through variation of the nominal composition both n-type and p-type conduction properties can be obtained.

In dieser Dissertation wird die Darstellung tetrelreicher Seltenerdmetall–Verbindungen in den Systemen SE:Tt (SE = La, Nd, Sm, Gd, Tb, Ho, Lu; Tt = Si, Ge) und die Charakterisierung ihrer Eigenschaften beschrieben. Diese Verbindungen, welche mittels der Hochdruck–Hochtemperatur–Methode dargestellt wurden, zeigen neuartige Verknüpfungsmuster in der Tetrel–Partialstruktur. Neben der Charakterisierung der Verbindungen hinsichtlich der thermischen Stabilität und der physikalischen Eigenschaften bei Normaldruck wurde bei den Germanium–reichen Seltenerdmetall–Verbindungen eine Untersuchung der Veränderungen der Kristallstruktur bei Variation des Drucks oder der Temperatur vorgenommen. Die dargestellten Seltenerdmetall–Trisilicide SESi3 (SE = Gd, Ho, Lu) kristallisieren tetragonal isotyp zu YbSi3. LuSi3 zeigt Supraleitung mit Tc = 7.0 K. In den Systemen Gd–Si und SE–Ge (SE = La, Nd, Sm, Gd, Tb) wurden die Verbindungen GdSi5 und SEGe5 (SE = La, Nd, Sm, Gd, Tb) synthetisiert. Sie kristallisieren orthorhombisch isotyp zu LaGe5. Durch in–situ Röntgenbeugungsexperimente bei erhöhten Temperaturen kann die Existenz metastabiler Germanium–ärmerer Verbindungen SE2Ge9 (SE = Nd, Sm) nachgewiesen werden. Es handelt sich um Defektvarianten der Verbindungen SEGe5 (SE = Nd, Sm). Die strukturelle Verwandtschaft zum Aristotyp SEGe5 wird anhand einer Gruppe–Untergruppe–Beziehung aufgezeigt. Eine alternative Synthesemethode zur Darstellung tetrelreicher Verbindungen mit Gerüststrukturen bei extremen Reaktionsbedingungen stellt das Spark–Plasma–Sinterverfahren (SPS) dar. Die Darstellung der Clathratphase Ba8Ga16±xGe30∓x (x = 0, 1) erfolgte mittels SPS aus den Precursoren BaGa2±x (x = 0, 0.125) und Germanium. Die Untersuchungen der thermoelektrischen Eigenschaften zeigen, dass durch Variation der nominellen Zusammensetzung sowohl n–leitende als auch p–leitende Eigenschaften erhalten werden können. / In this thesis the synthesis of tetrel–rich rare–earth metal compounds in the systems RE:Tt (RE = La, Nd, Sm, Gd, Tb, Ho, Lu; Tt = Si, Ge) and the characterization of their properties is described. These compounds, synthesized by means of high–pressure high–temperature method, show new structural motifs in the tetrel partial structure. The compounds were characterized with respect to their thermal stability and their physical properties at ambient pressure. In addition, the changes in the crystal structure of the germanium-rich rare–earth metal compounds by variation of pressure or temperature were investigated. The synthesized rare–earth trisilicides SESi3 (SE = Gd, Ho, Lu) crystallize tetragonal, isotypic to YbSi3. LuSi3 is a superconductor with Tc = 7.0 K. In the systems Gd–Si and SE–Ge (SE = La, Nd, Sm, Gd, Tb) the compounds GdSi5 and SEGe5 (SE = La, Nd, Sm, Gd, Tb) were synthesized. They crystallize orthorhombic isotypic to LaGe5. Using in-situ high–temperature X-ray experiments the metastable germanium-poorer compounds SE2Ge9 (SE = Nd, Sm) could be observed. These compounds are defect variants of the pentagermanides SEGe5 (SE = Nd, Sm). The structural relationship to the aristotype SEGe5 is given via a group-subgroup relation. An alternative synthesis route for the preparation of tetrel–rich compounds with framework structures at extreme reaction conditions is the spark plasma sintering method (SPS). The clathrate phase Ba8Ga16±xGe30∓x (x = 0, 1) was synthesized from the precursors BaGa2±x (x = 0, 0.125) and germanium by means of SPS. The investigation of the thermoelectric properties shows, that through variation of the nominal composition both n-type and p-type conduction properties can be obtained.

It is known that boron containing compounds exhibit interesting chemical and physical properties. In the past 50 years modern preparative methods have led to an overwhelming number of different structures of novel and often unexpected boron–sulfur and boron–selenium compounds. Among all these new compounds, there was only one which comprises rare earth metal (RE), boron and heavier chalcogen, namely sulfur, the europium thioborate Eu[B2S4] [1]. Selenoborates of rare earth metals are hitherto unknown. On the other hand, rare earth oxoborates represent a well-known class of compounds [2] with a wide range of applications, especially in the field of optical materials. In addition, well-defined boron compounds containing the heavier group 16 elements are fairly difficult to prepare due to the high reactivity of in situ formed boron chalcogenides towards most container materials at elevated temperatures. The chalcogenoborates of the heavier chalcogens are sensitive against oxidation and hydrolysis and therefore have to be handled in an inert environment. Therefore, developing and optimization of preparative routes for the syntheses of pure and crystalline RE thio- and selenoborates was needed. In the course of this study, the application of different preparation routes, such as optimized high-temperature routes (HT), metathesis reactions and high-pressure high-temperature routes (Hp – HT), led to sixteen new rare earth thioborates. Their crystal structures were solved and/or refined from powder and single crystal X-ray diffraction data, while the local structure around rare earth metal was confirmed from the results of the EXAFS analyses. Quantum mechanical calculations were used within this work in order to investigate the arrangement of intrinsic vacancies on the boron sites in the crystal structures of rare earth thioborates. Thermal, magnetic and optical properties of these compounds are also discussed. The rare earth thioborates discovered during this work are the first examples of ternary thioborates containing trivalent cations. These compounds can be divided into two groups of isotypic compounds: the rare earth orthothioborates with general formula REIII[BS3] (RE = La – Nd, Sm, Gd and Tb) [3] and the rare earth thioborate sulfides with general formula REIII¦9B5S21, (RE = Gd – Lu, and Y) [4]. In the crystal structure of RE[BS3] (orthorhombic, space group Pna21, Z = 4), the sulfur atoms form the vertices of corrugated kagome nets, within which every second triangle is occupied by boron and the large hexagons are centered by RE cations. The structural features of the isotypic RE[BS3] phases show great similarities to those of rare earth oxoborates RE[BO3] and orthothioborates of alkali and alkaline earth metals as well as to thallium orthothioborate, yet pronounced differences are also observed: the [BS3]3– groups in the crystal structures of RE[BS3] are more distorted, where the distortion decreases with the decreasing size of the RE element, and the coordination environments of the [BS3]3– groups in the crystal structures of RE[BS3] are different in comparison with the coordination environments of the [BO3]3– groups in the crystal structures of λ-Nd[BO3] [5] and of o-Ce[BO3] [6]. The results of the IR and Raman investigations are in agreement with the presence of [BS3]3– anions in the crystal structure of RE[BS3]. Thermal analyses revealed the thermal stability of these compounds under inert conditions up to ~ 1200 K. Analyses of the magnetic properties of the Sm, Gd and Tb thioborates showed that both Gd and Tb phases order antiferromagnetically. The magnetic susceptibility for Sm orthothioborate approximately follows the Van-Vleck theory for Sm3+. Between 50 K and 62 K a transition appears which is independent of the magnetic field: the magnetic susceptibility becomes lower. This effect might indicate a discontinuous valence transition of Sm which was further investigated by means of XANES and X-ray diffraction using synchrotron radiation, both at low temperatures. The series of isotypic RE thioborate sulfides with composition RE9B5S21, was obtained by the application of Hp – HT conditions to starting mixtures with the initial chemical composition “REB3S6“, after careful optimization of the pressure, temperature and treatment time, as well as the composition of the starting mixtures. Their crystal structures adopt the Ce6Al3.33S14 [7] structure type (hexagonal, space group P63, Z = 2/3). The special features of the RE9B5S21 crystal structures, concerning boron site occupancies and different coordination environments of the two crystallographically independent boron sites, were investigated in more detail by means of quantum chemical calculations, electron diffraction methods, optical and X-ray absorption spectroscopy as well as by 11B NMR spectroscopy. The results obtained from these different experimental and computational methods are in good mutual agreement. The crystal structures of the RE9B5S21 compounds are characterized by two types of anions: tetrahedral [BS4]5– and trigonal planar [BS3]3– as well as [(S2–)3] units. Isolated [BS4]5– tetrahedra (all pointing with one of their apices along the polar [001] direction) represent a unique feature of the crystal structure which is observed for the first time in a thioborate compound. These tetrahedra are stacked along the three-fold rotation axes. Vacancies are located at the trigonal-planar coordinated boron site with preferred ordering –B–B––B–B–– along [001]. No superstructure is observed by means of electron diffraction methods as adjacent columns are shuffled along the c axis, giving rise to a randomly distributed vacancy pattern. Positions of the sulfur atoms within the [(S2–)3] substructure as well as planarity of the [BS3]3– units were investigated in more detail by means of quantum mechanical calculations. Results of the IR and Raman spectroscopy, as well as of the 11B NMR spectroscopy are in agreement with the presence of the boron atoms in two different coordination environments. Thermal analyses showed that compounds RE9B5S21 are stable under inert conditions up to ~ 1200 K. In accordance with the combined results of experimental and computational investigations, the chemical formula of the RE9B5S21 compounds is consistent with RE3[BS3]2[BS4]3S3. A short overview of investigations towards rare earth selenoborates, where in most of the cases only known binary rare earth selenides could be identified, is presented as well in this work. Investigations in the RE–B–Se systems were conducted by the application of different preparation routes by varying the experimental parameters and the initial compositions of the starting mixtures. Although no crystal structure of a ternary phase in these systems could be solved, there are indications that such phases exist, but further investigations are needed. [1] M. Döch, A. Hammerschmidt, B. Krebs, Z. Anorg. Allg. Chem., 2004, 630, 519. [2] H. Huppertz, Chem. Commun., 2011, 47, 131; and references therein. [3] J. Hunger, M. Borna, R. Kniep, J. Solid State Chem., 2010, 182, 702; J. Hunger, M. Borna, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 217; M. Borna, J. Hunger, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 223; M. Borna, J. Hunger, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 225. [4] M. Borna, J. Hunger, A. Ormeci, D. Zahn, U. Burkhardt, W. Carrillo-Cabrera, R. Cardoso-Gil, R. Kniep, J. Solid State Chem., 2011, 184, 296; [5] H. Müller-Bunz, T. Nikelski, Th. Schleid, Z. Naturforsch. B, 2003, 58, 375. [6] H. U. Bambauer, J. Weidelt, J.-St. Ysker, Z. Kristallogr., 1969, 130, 207. [7] D. de Saint-Giniez, P. Laruelle, J. Flahaut, C. R. Séances, Acad. Sci. Ser. C, 1968, 267, 1029.

It is known that boron containing compounds exhibit interesting chemical and physical properties. In the past 50 years modern preparative methods have led to an overwhelming number of different structures of novel and often unexpected boron–sulfur and boron–selenium compounds. Among all these new compounds, there was only one which comprises rare earth metal (RE), boron and heavier chalcogen, namely sulfur, the europium thioborate Eu[B2S4] [1]. Selenoborates of rare earth metals are hitherto unknown. On the other hand, rare earth oxoborates represent a well-known class of compounds [2] with a wide range of applications, especially in the field of optical materials. In addition, well-defined boron compounds containing the heavier group 16 elements are fairly difficult to prepare due to the high reactivity of in situ formed boron chalcogenides towards most container materials at elevated temperatures. The chalcogenoborates of the heavier chalcogens are sensitive against oxidation and hydrolysis and therefore have to be handled in an inert environment. Therefore, developing and optimization of preparative routes for the syntheses of pure and crystalline RE thio- and selenoborates was needed. In the course of this study, the application of different preparation routes, such as optimized high-temperature routes (HT), metathesis reactions and high-pressure high-temperature routes (Hp – HT), led to sixteen new rare earth thioborates. Their crystal structures were solved and/or refined from powder and single crystal X-ray diffraction data, while the local structure around rare earth metal was confirmed from the results of the EXAFS analyses. Quantum mechanical calculations were used within this work in order to investigate the arrangement of intrinsic vacancies on the boron sites in the crystal structures of rare earth thioborates. Thermal, magnetic and optical properties of these compounds are also discussed. The rare earth thioborates discovered during this work are the first examples of ternary thioborates containing trivalent cations. These compounds can be divided into two groups of isotypic compounds: the rare earth orthothioborates with general formula REIII[BS3] (RE = La – Nd, Sm, Gd and Tb) [3] and the rare earth thioborate sulfides with general formula REIII¦9B5S21, (RE = Gd – Lu, and Y) [4]. In the crystal structure of RE[BS3] (orthorhombic, space group Pna21, Z = 4), the sulfur atoms form the vertices of corrugated kagome nets, within which every second triangle is occupied by boron and the large hexagons are centered by RE cations. The structural features of the isotypic RE[BS3] phases show great similarities to those of rare earth oxoborates RE[BO3] and orthothioborates of alkali and alkaline earth metals as well as to thallium orthothioborate, yet pronounced differences are also observed: the [BS3]3– groups in the crystal structures of RE[BS3] are more distorted, where the distortion decreases with the decreasing size of the RE element, and the coordination environments of the [BS3]3– groups in the crystal structures of RE[BS3] are different in comparison with the coordination environments of the [BO3]3– groups in the crystal structures of λ-Nd[BO3] [5] and of o-Ce[BO3] [6]. The results of the IR and Raman investigations are in agreement with the presence of [BS3]3– anions in the crystal structure of RE[BS3]. Thermal analyses revealed the thermal stability of these compounds under inert conditions up to ~ 1200 K. Analyses of the magnetic properties of the Sm, Gd and Tb thioborates showed that both Gd and Tb phases order antiferromagnetically. The magnetic susceptibility for Sm orthothioborate approximately follows the Van-Vleck theory for Sm3+. Between 50 K and 62 K a transition appears which is independent of the magnetic field: the magnetic susceptibility becomes lower. This effect might indicate a discontinuous valence transition of Sm which was further investigated by means of XANES and X-ray diffraction using synchrotron radiation, both at low temperatures. The series of isotypic RE thioborate sulfides with composition RE9B5S21, was obtained by the application of Hp – HT conditions to starting mixtures with the initial chemical composition “REB3S6“, after careful optimization of the pressure, temperature and treatment time, as well as the composition of the starting mixtures. Their crystal structures adopt the Ce6Al3.33S14 [7] structure type (hexagonal, space group P63, Z = 2/3). The special features of the RE9B5S21 crystal structures, concerning boron site occupancies and different coordination environments of the two crystallographically independent boron sites, were investigated in more detail by means of quantum chemical calculations, electron diffraction methods, optical and X-ray absorption spectroscopy as well as by 11B NMR spectroscopy. The results obtained from these different experimental and computational methods are in good mutual agreement. The crystal structures of the RE9B5S21 compounds are characterized by two types of anions: tetrahedral [BS4]5– and trigonal planar [BS3]3– as well as [(S2–)3] units. Isolated [BS4]5– tetrahedra (all pointing with one of their apices along the polar [001] direction) represent a unique feature of the crystal structure which is observed for the first time in a thioborate compound. These tetrahedra are stacked along the three-fold rotation axes. Vacancies are located at the trigonal-planar coordinated boron site with preferred ordering –B–B––B–B–– along [001]. No superstructure is observed by means of electron diffraction methods as adjacent columns are shuffled along the c axis, giving rise to a randomly distributed vacancy pattern. Positions of the sulfur atoms within the [(S2–)3] substructure as well as planarity of the [BS3]3– units were investigated in more detail by means of quantum mechanical calculations. Results of the IR and Raman spectroscopy, as well as of the 11B NMR spectroscopy are in agreement with the presence of the boron atoms in two different coordination environments. Thermal analyses showed that compounds RE9B5S21 are stable under inert conditions up to ~ 1200 K. In accordance with the combined results of experimental and computational investigations, the chemical formula of the RE9B5S21 compounds is consistent with RE3[BS3]2[BS4]3S3. A short overview of investigations towards rare earth selenoborates, where in most of the cases only known binary rare earth selenides could be identified, is presented as well in this work. Investigations in the RE–B–Se systems were conducted by the application of different preparation routes by varying the experimental parameters and the initial compositions of the starting mixtures. Although no crystal structure of a ternary phase in these systems could be solved, there are indications that such phases exist, but further investigations are needed. [1] M. Döch, A. Hammerschmidt, B. Krebs, Z. Anorg. Allg. Chem., 2004, 630, 519. [2] H. Huppertz, Chem. Commun., 2011, 47, 131; and references therein. [3] J. Hunger, M. Borna, R. Kniep, J. Solid State Chem., 2010, 182, 702; J. Hunger, M. Borna, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 217; M. Borna, J. Hunger, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 223; M. Borna, J. Hunger, R. Kniep, Z. Kristallogr. NCS, 2010, 225, 225. [4] M. Borna, J. Hunger, A. Ormeci, D. Zahn, U. Burkhardt, W. Carrillo-Cabrera, R. Cardoso-Gil, R. Kniep, J. Solid State Chem., 2011, 184, 296; [5] H. Müller-Bunz, T. Nikelski, Th. Schleid, Z. Naturforsch. B, 2003, 58, 375. [6] H. U. Bambauer, J. Weidelt, J.-St. Ysker, Z. Kristallogr., 1969, 130, 207. [7] D. de Saint-Giniez, P. Laruelle, J. Flahaut, C. R. Séances, Acad. Sci. Ser. C, 1968, 267, 1029.:I INTRODUCTION ......................................................................... 7 1. Motivation and scope of the work .............................................. 9 2. Literature overview .................................................................. 11 2.1. The binary subsystems of the ternary systems RE–B–Q (RE = rare earth metals, Y; Q = S, Se) ......................................................... 12 2.1.1. RE–Q ............................................................................... 12 2.1.2. RE–B ............................................................................... 19 2.1.3. B–Q ................................................................................. 22 2.2. Related ternary compounds ................................................... 25 2.2.1. RE oxoborates .................................................................. 25 2.2.2. Thio- and selenoborates of alkaline, alkaline earth, transition and post transition metals ......................................................................... 33 2.2.3. The RE thioborate Eu[B2S4]................................................ 45 II PREPARATIVE METHODS AND EXPERIMENTAL TECHNIQUES .......... 47 1. Starting materials and their characterization ............................... 49 2. Synthetic approaches and optimizations .................................... 51 2.1. High-temperature routes ...................................................... 52 2.2. Metathesis reactions ............................................................ 53 2.3. Spark Plasma Sintering (SPS) ............................................... 54 2.4. High-Pressure High-Temperature (Hp – HT) Syntheses ........... 55 3. Analytical methods and samples characterization ....................... 55 3.1. Powder X-ray diffraction ...................................................... 55 3.2. Crystal structure investigations using synchrotron radiation .... 57 3.3. Single crystal X-ray diffraction analysis .................................. 57 3.4. Metallographic investigations ................................................ 58 3.5. Electron microscopy ............................................................ 58 3.5.1. Scanning electron microscopy and energy dispersive X-ray spectroscopy ............................................................................ 58 3.5.2. Transmission electron microscopy ...................................... 59 3.6. Optical spectroscopy ........................................................... 59 3.6.1. Infra-Red spectroscopy .................................................... 59 3.6.2. Raman spectroscopy ........................................................ 60 3.7. X-ray absorption spectroscopy ............................................ 60 3.8. Thermal analysis ................................................................. 62 3.9. Magnetic susceptibility measurements ................................... 63 3.10. 11B NMR spectroscopy ..................................................... 63 3.11. Quantum chemical calculations ........................................... 64 3.11.1. Total energy calculations ................................................ 64 3.11.2. Charge transfer analysis ................................................ 64 3.11.3. Chemical bonding........................................................... 64 III RARE EARTH THIOBORATES ................................................. 67 1. Reinvestigation of the only reported rare earth thioborate – EuB2S4 ....69 2. RE[BS3] (RE = La – Nd, Sm, Gd, Tb) .................................... 69 2.1. Syntheses and phase analyses .......................................... 70 2.2. Crystal structure determinations ........................................ 74 2.3. X-ray absorption spectroscopy: EXAFS data analysis for Pr[BS3] ..... 79 2.4. Crystal chemistry .............................................................. 80 2.5. Optical spectroscopy ......................................................... 83 2.6. Thermal analysis ............................................................... 86 2.7. Magnetic susceptibility ....................................................... 88 2.8. X-ray absorption spectroscopy: XANES data analysis for Sm[BS3] .. 91 2.9. Crystal structure investigation at low temperature using synchrotron radiation ................................................................................... 91 2.10. Summary ......................................................................... 95 3. Gd[BS3] : Ce, Eu, Tb ............................................................. 97 3.1. Syntheses and phase analyses ............................................. 97 3.2. Crystal structure determinations ......................................... 101 3.3. Crystal chemistry .............................................................. 103 3.4. Optical spectroscopy ......................................................... 104 3.5. Thermal analysis ............................................................... 106 3.6. Summary ......................................................................... 107 4. RE9B5S21 (RE = Tb – Lu, Y) ................................................ 107 4.1. Syntheses and phase analyses ........................................... 108 4.2. Crystal structure determinations ........................................ 109 4.3. Crystal chemistry .............................................................. 112 4.4. Electronic structure, charge transfer and chemical bonding .... 115 4.5. X-ray absorption spectroscopy: EXAFS data analysis for Lu9B5S21 .............................................................................. 119 4.6. Thermal analysis ............................................................... 121 4.7. 11B NMR investigations ..................................................... 122 4.8. Optical spectroscopy ......................................................... 123 4.9. Summary ......................................................................... 126 IV ON THE WAY TO RARE EARTH SELENOBORATES .................... 127 1. Towards ternary phases in the systems RE–B–Se, with RE = Sm, Tb – Lu.......................................................................................... 129 2. The system La–B–Se ........................................................... 134 3. The system Gd–B–Se .......................................................... 136 4. The system Y–B–Se ............................................................ 137 5. Summary ........................................................................... 139 V SUMMARY AND OUTLOOK ..................................................... 141 VI APPENDIX .......................................................................... 149 VII REFERENCES .................................................................... 163 VIII LIST OF FIGURES ............................................................. 181 IX LIST OF TABLES ................................................................ 193 X CURRICULUM VITAE ........................................................... 199 XI VERSICHERUNG ............................................................... 203

Ziel der Arbeit war die Synthese von ZnS, welches strukturell natürlichen Sphalerit imitieren und für die Untersuchung und Optimierung von biologischen Laugungsexperimenten genutzt werden soll. Zur Herstellung von chemisch reinem sowie mit den Wertelementen Indium, Kupfer und Eisen dotierten ZnS wurden vier verschiedene Synthesemethoden getestet: Ofentempern, chemische Gasphasentransportreaktion (CVT), feldunterstütztes Sintern (SPS) und die Hochdruck-Hochtemperatur-Synthese (HP/HT). Es folgte die Charakterisierung der synthetisierten Produkte hinsichtlich der Realstruktur und chemischen Reinheit mittels XANES, REM, XRD, EPMA und nasschemischer Verfahren. Abschließend wurden die Synthesemethoden nach ihrer Effizienz evaluiert. Das Ziel, defektfreies kubisches ZnS zu erzeugen, wurde nur mittels CVT und HP/HT erreicht. In dieser Arbeit konnte weiterhin gezeigt werden, dass der Einbau von Indium ohne gleichzeitige Aufnahme von Kupfer bis zu 1 Ma-% möglich ist.:Abbildungsverzeichnis VII Tabellenverzeichnis XI Abkürzungen, Akronyme und Symbole XII Einheiten XV 1 Einleitung 1 2 Forschungsstand zur Synthese von Zinksulfid 6 2.1 Kristallographie von ZnS . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 8 2.2 p-T -Phasendiagramm von ZnS . . . . . . . . . . . . . . . . . . . . . . . . . . . 12 3 Synthesematerial 15 3.1 Gefälltes ZnS . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 15 3.2 Dotierungsmaterialien . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 17 3.3 Recherche zu kommerziellen Metallsulfiden . . . . . . . . . . . . . . . . . . . . 18 4 Synthesemethoden 21 4.1 Ofentempern . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 22 4.2 FAST-SPS . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 23 4.3 CVT . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 24 4.4 HP/HT-Synthese . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 26 4.4.1 Toroid-Zelle . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 26 4.4.2 HP/HT-Experimentalaufbau und -ablauf . . . . . . . . . . . . . . . . . 27 4.4.3 HP/HT-Kalibrierung . . . . . . . . . . . . . . . . . . . . . . . . . . . . 32 5 Analysemethoden 42 5.1 ICP-MS & ICP-OES . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 43 5.2 XRD . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 44 5.3 UV-VIS . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 55 5.4 REM-EDX . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 55 5.5 EBSD . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 56 5.6 EPMA . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 57 5.7 XANES Spektroskopie . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 58 5.8 Ramanspektroskopie . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 61 5.9 Dichtebestimmung . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 62 5.10 BET-Messung . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 62 6 Ergebnisse 63 6.1 Charakterisierung industriell verfügbarer Materialien und natürlicher Proben . 63 6.1.1 Synthetische, industriell verfügbare Materialien . . . . . . . . . . . . . . 63 6.1.2 Referenzspektren für XANES-Analysen . . . . . . . . . . . . . . . . . . 65 6.2 Charakterisierung der Synthesematerialien . . . . . . . . . . . . . . . . . . . . 74 6.2.1 ZnS der Leuchtstoffwerke Breitungen GmbH (LWB) . . . . . . . . . . . 74 6.2.2 Dotierungsmaterialien In, Cu und Fe . . . . . . . . . . . . . . . . . . . . 77 6.3 Charakterisierung der synthetisierten Produkte . . . . . . . . . . . . . . . . . . 80 6.3.1 Einkristalle (CVT) . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 80 6.3.2 Polykristalline Produkte (Ofentempern, FAST-SPS und HP/HT) . . . . 112 6.4 Bestimmung des Stapelfehleranteils mittels Ramanspektroskopie? . . . . . . . . 152 7 Diskussion 155 7.1 Synthesematerialien und industriell verfügbare Materialien . . . . . . . . . . . 155 7.2 Syntheseprodukte . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 160 7.2.1 Syntheseprodukte: Einkristalle (CVT) . . . . . . . . . . . . . . . . . . . 160 7.2.2 Syntheseprodukte: Polykristalline Produkte (Ofentempern, FAST-SPS und HP/HT) . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . . 183 7.2.3 Vergleich der Syntheseprodukte: Einkristalle und Polykristalline Produkte 202 8 Laugungsexperimente: Zusammenfassung und Schlussfolgerung 213 9 Schlussfolgerung 220 10 Zusammenfassung 221 Literaturverzeichnis 225 Anhang A Ergebnispräsentation auf internationalen Fachtagungen 247 B Pulver vs. Kompaktprobe-Diffraktometrie 249 C ZnSdis.str-Datei 252 D Bestimmung der Bandlücke 254 E Messpunkte EPMA 256 F Einwaagen der Synthese 258 G Texturfaktoren der Röntgenbeugung X-Ray Diffraction (XRD)-Analyse 260