The fracture of water ballast tank (WBT) coatings due to thermal stresses is widely recognised as an issue. Upon coating fracture, rapid corrosion of the tanker steel structure will occur, leading to expensive structure repairs or even tanker scrapping. In this project, the fracture behaviour of two experimental WBT coatings, referred to as A and B, in the forms of free film and substrated coatings was investigated. Static tensile tests and fatigue tests of the substrated coatings were performed. A finite element model of coating cracking was developed. Thermal stress and J-integral of surface cracking defects in substrated coatings were calculated using the model, in which the effects of defect size, coating thickness, and thermal strain on coating fracture were investigated. For the first time, fracture mechanics was used to explain WBT coating fracture behaviour. The J-integral of surface defects was used to predict the onset strain of coating cracking under mechanical strains in laboratory and under thermal strains in service. A theoretical comparison between the cracking drive forces in terms of J - integrals in WBT coatings under thermal strains and mechanical strains was performed.

Thermal management in electronic devices is one of the biggest challenges faced by the semiconductor industry. Thermal Interface Materials (TIMs) are used in electronics to fill air gaps between the surfaces of integrated circuit (IC) chips to dissipate heat. Polymer-graphene composites, a very promising choice as TIMs also have a drawback of high interfacial thermal resistance and a low thermal conductivity of polymer. It is known from the theoretical models that application of pressure may affect the thermal conductivity in a desirable manner, but quantitative simulations were not available. In this paper, the pressure dependence of thermal conductivity of epoxy and interfacial resistance at epoxy-graphene interface is studied using non-equilibrium molecular dynamics (NEMD) simulations. The results show that the thermal conductivity of epoxy increases with increase in pressure, and they compare well with the predictions using a theoretical model. The interfacial thermal resistance at epoxy-graphene interface reduces with increase in pressure. The reduction is sharp in the beginning and slowly reaches saturation as pressure increases. At 10 GPa compressive pressure, a 90-95% decrease in interfacial thermal resistance is observed.

Yin, Weixin = 非晶液態鈀-鎳-磷合金相位分離的證據 / 殷瑋欣. / Thesis (M.Phil.)--Chinese University of Hong Kong, 2011. / Includes bibliographical references. / Abstracts in English and Chinese. / Yin, Weixin = Fei jing ye tai ba-nie-lin he jin xiang wei fen li de zheng ju / Yin Weixin. / Acknowledgement --- p.i / Abstract --- p.ii / Contents --- p.iv / Chapter Chapter 1 --- Introduction --- p.1 / Chapter 1.1 --- A Brief Introduction to Metallic Glass --- p.1 / Chapter 1.2 --- Homogeneous Nucleation Frequency --- p.3 / Chapter 1.3 --- Heterogeneous Nucleation Frequency --- p.4 / Chapter 1.4 --- Spinodal Decomposition --- p.5 / Chapter 1.5 --- Conditions for Metallic Glasses Formation --- p.8 / Chapter 1.6 --- How to Get Large Undercooling --- p.9 / Chapter 1.7 --- Liquid Phase Separation --- p.10 / References --- p.12 / Figures --- p.13 / Chapter Chapter 2 --- Experimental Procedures and Techniques of Transmission Electron Microscopy --- p.18 / Chapter 2.1 --- Sample preparation --- p.18 / Chapter 2.1.1 --- Ni2P Preparation --- p.18 / Chapter 2.1.2 --- Alloying --- p.18 / Chapter 2.1.3 --- Fluxing --- p.18 / Chapter 2.2 --- Introduction to TEM Specimen Preparation --- p.19 / Chapter 2.2.1 --- "Grinding, Polishing and Punching" --- p.19 / Chapter 2.2.2 --- Final Thinning by Ion Miller --- p.20 / Chapter 2.2.3 --- Final Thinning by Twin Jet --- p.20 / Chapter 2.3 --- Introduction to Transmission Electron Microscopy Techniques --- p.21 / Chapter 2.3.1 --- Basic Instrumentations of TEM --- p.21 / Chapter 2.3.2 --- Elastic Scattering and Inelastic Scattering --- p.21 / Chapter 2.3.3 --- Image Contrast --- p.22 / Chapter 2.3.4 --- Dark Field Image and Bright Field Image --- p.24 / Chapter 2.3.5 --- EDX Mapping --- p.24 / Chapter 2.3.6 --- High Resolution Images --- p.25 / References --- p.26 / Figures --- p.27 / Chapter Chapter 3 --- Evidence of amorphous/liquid phase separation in Pd41.25Ni41.25P17.5 alloy --- p.32 / Chapter 3.1 --- Introduction --- p.32 / Chapter 3.2 --- Experimental --- p.34 / Chapter 3.3 --- Discussions --- p.42 / References --- p.44 / Figures --- p.45 / Chapter Chapter 4 --- Conclusions --- p.68

過去幾十年當中，金屬玻璃（包括塊狀金屬玻璃）中非晶相分離的發生已經成為了一個具有爭議性的課題。一些報告報導在具有負混合熱的Pd-Ni-P合金體系中發生了非晶相分離。然而，有一些報告聲稱相分離不能在Pd-Ni-P非晶合金中被觀察到。文獻分析表明，困難在於缺乏直接的實驗證據。 / 為了解決這個難題，示差掃描量熱儀、高分辨電子顯微鏡、掃描透射模式下的高角環射暗場相、以及能量色散X射線光譜儀等檢測儀器在我們實驗當中被使用。同時為了清楚展示非晶相分離反應，在過冷Pd₄₁.₂₅Ni₄₁.₂₅P₁₇.₅熔體被冷卻為固態非晶樣品之前引入了中間熱退火處理。 / 實驗研究了三種經由不同路徑製備的A、B、C型號樣品。結果表明在非晶/液態Pd₄₁.₂₅Ni₄₁.₂₅P₁₇.₅合金中可能存在獨特的短程有序結構，它會導致相分離的發生。同时研究發現，在大約625 K，調幅分解的持續時間的下限大概是200 s。調幅分解的時間常數R在大約625 K 下為0.002 s⁻¹。三种类型样品在不同的溫度下被退火從而獲得部分的結晶。A型號和B型號具有相似的行為。在低溫下，圓形的核心首先形成，接著發生共晶反應。在高溫下，出現了一種形狀為立方體的析出相。在C型號的樣品當中，核心和立方的析出物同時被發現。但是核心的成分分佈與A和B型號中出現的不同。同時，隨著退火時間的加長形核的數量也具有獨特的行為表現。作為對比，Pd₄₀Ni₄₀P₂₀塊狀金屬玻璃的結晶行為也被展開了研究。同樣的，以形成核心開始，但是它的成分分佈異於A和B型號的樣品。 / Amorphous phase separation in metallic glass (including bulk metallic glass) has been a controversial issue in the past several decades. There are reports saying that amorphous phase separation occurs in Pd-Ni-P, which has a negative heat of mixing among its constituent elements. However, there are also as many reports claiming that phase separation is absent in amorphous Pd-Ni-P alloys. The lack of direct experimental evidence makes the issue to be difficult to be resolved. / To solve this problem, differential scanning calorimetry (DSC), high resolution transmission electron microscopy (HRTEM), high angle annular dark field (HAADF) in scanning transmission electron microscopy, and energy dispersive X-ray spectroscopy (EDX) have been employed. Intermediate thermal annealing is introduced before an undercooled Pd₄₁.₂₅Ni₄₁.₂₅P₁₇.₅ melt is cooled down to become a solid amorphous specimen. / A-type, B-type, and C-type specimens of composition, Pd₄₁.₂₅Ni₄₁.₂₅ P₁₇.₅, have been prepared via three different cooling paths. It was found that amorphous phase separation indeed occurs in C-type specimens. Results suggest that there may be unique short range orders in amorphous/liquid Pd₄₁.₂₅Ni₄₁.₂₅P₁₇.₅, which are responsible for the phase separation. Experimental arrangements were made to study the occurrence of spinodal reaction in undercooled molten Pd₄₁.₇₅Ni₄₁.₇₅P₁₇.₅ alloys as a function of time. The lower bound of the duration of the spinodal decomposition at a temperature of {U+2248}625 K is about 200 s and the time constant R of the spinodal decomposition at a temperature of {U+2248}625 K is 0.002 s⁻¹. / A-type and B-type specimens have similar crystallization behavior. At low temperature, it starts with the formation of a spherical core and then eutectic crystallization takes over. At higher temperatures, an additional phase in the shape of a cube appears. In annealed C-type specimens, cores and cubic precipitates are also found. However, the composition profile of the cores is different and the number of nucleation events versus time has peculiar characteristics. The crystallization behavior of Pd₄₀Ni₄₀P₂₀ BMG was studied for comparison. It again starts out with the formation of a core, but with a composition profile different from those of A-type and B-type specimens. / Detailed summary in vernacular field only. / Detailed summary in vernacular field only. / Detailed summary in vernacular field only. / Lan, Si = 對於具有負混合熱的塊狀金屬玻璃非晶相分離的研究 / 蘭司. / Thesis (Ph.D.)--Chinese University of Hong Kong, 2012. / Includes bibliographical references. / Abstract also in Chinese. / Lan, Si = Dui yu ju you fu hun he re de kuai zhuang jin shu bo li fei jing xiang fen li de yan jiu / Lan Si. / Abstract of thesis --- p.i / Acknowledgements --- p.v / List of Tables --- p.x / List of Figures --- p.xi / Chapter Chapter 1 --- Introduction and literature review --- p.1 / Chapter 1.1 --- Introduction to metallic glasses --- p.1 / Chapter 1.1.1 --- Background of metallic glasses --- p.1 / Chapter 1.1.2 --- Glass transition --- p.2 / Chapter 1.1.3 --- The undercooling of liquids --- p.3 / Chapter 1.1.4 --- Crystal nucleation and growth in liquids --- p.3 / Chapter 1.1.4.1 --- Crystal Nucleation in liquids --- p.3 / Chapter 1.1.4.2 --- Crystal growth in liquids --- p.5 / Chapter 1.1.4.3 --- TTT diagram --- p.6 / Chapter 1.1.4.4 --- Crystallization in metallic glasses --- p.6 / Chapter 1.1.5 --- Glass formation methods and systems --- p.6 / Chapter 1.1.6 --- Glass forming ability and criteria --- p.8 / Chapter 1.1.7 --- Properties and applications --- p.9 / Chapter 1.2 --- The basic theory of phase separation in a binary system --- p.10 / Chapter 1.2.1 --- Thermodynamic background --- p.10 / Chapter 1.2.2 --- Solid state phase separation --- p.11 / Chapter 1.2.2.1 --- A miscibility gap of binary mixture --- p.11 / Chapter 1.2.2.2 --- Nucleation and growth mechanism --- p.12 / Chapter 1.2.2.3 --- Spinodal decomposition mechanism --- p.13 / Chapter 1.2.3 --- Liquid state miscibility gap in a binary system --- p.21 / Chapter 1.3 --- Literature review for phase separation in metallic glasses --- p.23 / Chapter 1.4 --- The aim of this thesis --- p.28 / Figures --- p.30 / References --- p.39 / Chapter Chapter 2 --- Experiments and characterization --- p.44 / Chapter 2.1 --- Introduction and the outline of the experiments --- p.44 / Chapter 2.2 --- Sample preparation --- p.45 / Chapter 2.2.1 --- Bulk metallic glasses preparation --- p.45 / Chapter 2.2.1.1 --- Preparation of clean fused silica tubes --- p.45 / Chapter 2.2.1.2 --- Weighing --- p.46 / Chapter 2.2.1.3 --- Alloying --- p.46 / Chapter 2.2.1.4 --- Fluxing --- p.47 / Chapter 2.2.2 --- Thermal annealing --- p.49 / Chapter 2.2.3 --- Specimens preparation for characterization --- p.50 / Chapter 2.2.3.1 --- Cutting, molding, grinding and polishing --- p.50 / Chapter 2.2.3.2 --- Etching --- p.51 / Chapter 2.2.3.3 --- Thinning for TEM foils --- p.51 / Chapter 2.3 --- Characterization --- p.55 / Chapter 2.3.1 --- Differential scanning calorimetry (DSC) --- p.55 / Chapter 2.3.2 --- Scanning electron microscopy (SEM) --- p.55 / Chapter 2.3.3 --- Transmission electron microscopy (CTEM and HRTEM) --- p.57 / Chapter 2.3.4 --- High angle annular dark field (HAADF) in Scanning transmission electron microscopy (STEM) --- p.58 / Chapter 2.3.5 --- Energy dispersive X-ray spectroscopy (EDX) --- p.59 / Figures --- p.62 / References --- p.69 / Chapter 3 --- p.70 / Chapter 3.1 --- Introduction --- p.70 / Chapter 3.2 --- Materials and Experimental --- p.73 / Chapter 3.3 --- Results --- p.75 / Chapter 3.3.1 --- Thermal behaviors of three types of specimens --- p.75 / Chapter 3.3.2 --- Microstructures of three types of specimens --- p.75 / Chapter 3.3.2.1 --- A-type specimens --- p.75 / Chapter 3.3.2.2 --- B-type specimens --- p.76 / Chapter 3.3.2.3 --- C-type specimens --- p.76 / Chapter 3.4 --- Discussion --- p.78 / Chapter 3.5 --- Conclusions --- p.79 / Chapter 3.6 --- Afterward --- p.79 / Figures --- p.80 / References --- p.89 / Chapter Chapter 4 --- The time constant of the spinodal decomposition in Pd₄₁.₇₅Ni₄₁.₇₅P₁₇.₅ bulk metallic glasses --- p.92 / Chapter 4.1 --- Introduction --- p.92 / Chapter 4.2 --- Materials and experimental --- p.92 / Chapter 4.3 --- Results --- p.94 / Chapter 4.3.1 --- Thermal behaviors --- p.94 / Chapter 4.3.2 --- Microstructures --- p.94 / Chapter 4.4 --- Discussion --- p.96 / Chapter 4.5 --- Conclusions --- p.98 / Figures --- p.100 / References --- p.123 / Chapter Chapter 5 --- Crystallization in homogeneous and phase-separated Pd₄₁.₂₅Ni₄₁.₂₅P₁₇.₅ bulk metallic glasses --- p.125 / Chapter 5.1 --- Introduction --- p.125 / Chapter 5.2 --- Experiments --- p.126 / Chapter 5.3 --- Results --- p.128 / Chapter 5.3.1 --- Low temperature thermal annealing at 613 K with 0≤t{U+2090} ≤ 8 h --- p.128 / Chapter 5.3.1.1 --- A-type and B-type specimens --- p.128 / Chapter 5.3.1.2 --- C-type specimens --- p.130 / Chapter 5.3.1.3 --- Pd₄₀Ni₄₀P₂₀ BMG --- p.132 / Chapter 5.3.2 --- High temperature thermal annealing --- p.133 / Chapter 5.3.2.1 --- A-type and B-type specimens --- p.133 / Chapter 5.3.2.2 --- C-type specimens --- p.135 / Chapter 5.3.2.3 --- Pd₄₀Ni₄₀P₂₀ BMG --- p.137 / Chapter 5.4 --- Discussion --- p.137 / Chapter 5.4.1 --- Formation of spherical cores --- p.138 / Chapter 5.4.1.1 --- A-type and B-type Pd₄₁.₇₅Ni₄₁.₇₅P₁₇.₅ specimens --- p.138 / Chapter 5.4.1.2 --- C-type Pd₄₁.₇₅Ni₄₁.₇₅P₁₇.₅ specimens --- p.139 / Chapter 5.4.1.3 --- Pd₄₀Ni₄₀P₂₀ BMG --- p.140 / Chapter 5.4.2 --- Formation of cubic precipitates --- p.141 / Tables --- p.142 / Figures --- p.144 / References --- p.188 / Chapter Chapter 6 --- Conclusions --- p.190 / Bibliography --- p.192

by Yuen Cheong Wing. / Thesis (M.Phil.)--Chinese University of Hong Kong, 1996. / Includes bibliographical references (leaves [138]-[142]). / by Yuen Cheong Wing. / Acknowledgments --- p.ii / Abstract --- p.iii / Table of Contents --- p.v / Chapter Chapter 1: --- Introduction --- p.1-1 / Chapter 1.1 --- What is Metallic Glass? --- p.1-1 / Chapter 1.2 --- Use of Metallic Glass --- p.1-3 / Chapter 1.3 --- A Dilemma --- p.1-4 / Chapter 1.4 --- Glass Forming Ability --- p.1-5 / Chapter 1.5 --- Role of Liquid State Phase Separation in GFA --- p.1-6 / References --- p.1-9 / Figure --- p.1-10 / Chapter Chapter 2: --- Phase Separation Theory --- p.2-1 / Chapter 2.1 --- Free Energy Curve --- p.2-1 / Chapter 2.2 --- Nucleation and Growth --- p.2-2 / Chapter 2.2.1 --- Liquid state nucleation and growth --- p.2-2 / Chapter 2.2.2 --- Nucleation and growth during solidification --- p.2-4 / Chapter 2.3 --- Spinodal Decomposition --- p.2-5 / Chapter 2.3.1 --- Cahn-Hilliard linearized equation --- p.2-6 / Chapter 2.3.2 --- Temporal evolution --- p.2-9 / References --- p.2-12 / Figures --- p.2-15 / Chapter Chapter 3 ： --- Experimental Setup and Techniques --- p.3-1 / Chapter 3.1 --- Technique in Achieving High Undercooling --- p.3 -1 / Chapter 3.1.1 --- Effects and limitation of B203 --- p.3-1 / Chapter 3.1.2 --- Preparation of B203 --- p.3-3 / Chapter 3.1.3 --- Cleansing of apparatus --- p.3-4 / Chapter 3.2 --- Experimental --- p.3-5 / Chapter 3.2.1 --- Sample preparation --- p.3-6 / Chapter 3.2.2 --- Experimental setup --- p.3-7 / Chapter 3.2.3 --- Procedures --- p.3-8 / Chapter 3.3 --- Observing the Microstructure --- p.3-9 / Chapter 3.3.1 --- Cutting --- p.3-10 / Chapter 3.3.2 --- Molding --- p.3-10 / Chapter 3.3.3 --- Polishing --- p.3-11 / Chapter 3.3.4 --- Etching --- p.3-12 / Chapter 3.3.5 --- Observation --- p.3-12 / References --- p.3-14 / Table --- p.3-15 / Figures --- p.3-16 / Chapter Chapter 4: --- Metastable liquid phase separationin undercooled molten PD40. 5]\l40.5P19 --- p.4-1 / Abstract --- p.4-1 / References --- p.4-9 / Figures --- p.4-10 / Chapter Chapter 5 ： --- Transformation in undercooled molten PD40.5NI40.5P19 --- p.5-1 / Chapter 5.1 --- Abstract --- p.5-1 / Chapter 5.1 --- Introduction --- p.5-2 / Chapter 5.3 --- Experimental --- p.5-4 / Chapter 5.4 --- Results --- p.5-6 / Chapter 5.5 --- Discussions --- p.5-13 / References --- p.5-20 / Figures --- p.5-22 / Chapter Chapter 6 ： --- Solidification of liquid spinodal in undercooled PD40.5NI40.5P19 --- p.6-1 / Chapter 6.1 --- Abstract --- p.6-1 / Chapter 6.2 --- Introduction --- p.6-2 / Chapter 6.3 --- Experimental --- p.6-3 / Chapter 6.4 --- Results --- p.6-5 / Chapter 6.5 --- Discussions --- p.6-10 / References --- p.6-17 / Figures --- p.6-18 / Chapter Chapter 7: --- Conclusion --- p.7-1 / References --- p.7-4 / Bibliography --- p.B-1

by Kwong Wai Kuen = 鋁銘金屬間化合物的製造和性能測試 / 鄺偉權. / Thesis (M.Phil.)--Chinese University of Hong Kong, 2003. / Includes bibliographical references. / Text in English; abstracts in English and Chinese. / by Kwong Wai Kuen = Lü ming jin shu jian hua he wu de zhi zao he xing neng ce shi / Kuang Weiquan. / Acknowledgement --- p.i / Abstract --- p.ii / 摘要 --- p.iii / List of tables --- p.iv / List of figures --- p.v / Table of contents --- p.xi / Chapter Chapter 1 --- Background / Chapter 1.1 --- Introduction --- p.1-1 / Chapter 1.2 --- Aluminum --- p.1-1 / Chapter 1.3 --- Chromium --- p.1-3 / Chapter 1.4 --- Intermetallics --- p.1-4 / Chapter 1.4.1 --- Alloys and intermetallics --- p.1-4 / Chapter 1.4.2 --- Properties of intermetallics --- p.1-5 / Chapter 1.4.3 --- Intermetallics 一 past to present --- p.1-6 / Chapter 1.4.4 --- Commonly used intermetallics --- p.1-7 / Chapter 1.4.5 --- Prospects of intermetallic compounds --- p.1-9 / Chapter 1.5 --- Previous works --- p.1-11 / Chapter 1.6 --- Current work --- p.1-12 / Chapter 1.7 --- Outline of thesis --- p.1-12 / References --- p.1-14 / Tables and figures --- p.1-17 / Chapter Chapter 2 --- Methodology and Instrumentation / Chapter 2.1 --- Experimental approaches --- p.2-1 / Chapter 2.2 --- Sample preparation --- p.2-2 / Chapter 2.2.1 --- Powder mixture --- p.2-2 / Chapter 2.2.2 --- Cold-pressing --- p.2-2 / Chapter 2.2.3 --- Pressureless sintering --- p.2-2 / Chapter 2.2.4 --- Hot-pressing --- p.2-3 / Chapter 2.2.5 --- Arc-melting --- p.2-4 / Chapter 2.3 --- Sample characterization --- p.2-5 / Chapter 2.3.1 --- DTA --- p.2-5 / Chapter 2.3.2 --- TMA --- p.2-5 / Chapter 2.3.3 --- Density measurement --- p.2-6 / Chapter 2.3.4 --- Microhardness measurement --- p.2-7 / Chapter 2.3.5 --- Scanning electron microscopy --- p.2-8 / Chapter 2.3.6 --- X-ray powder diffractometry --- p.2-9 / References --- p.2-10 / Figures --- p.2-11 / Chapter Chapter 3 --- Thermal analysis of Al-Cr powder mixtures / Chapter 3.1 --- Introduction --- p.3-1 / Chapter 3.2 --- Experiments --- p.3-1 / Chapter 3.3 --- Results and discussions --- p.3-2 / Chapter 3.3.1 --- DTA results --- p.3-2 / Chapter 3.3.2 --- Al-23wt%Cr --- p.3-2 / Chapter 3.3.3 --- Al-28wt%Cr and Al-33wt%Cr --- p.3-5 / Chapter 3.3.4 --- Al-46wt%Cr --- p.3-8 / Chapter 3.3.5 --- Al-55wt%Cr --- p.3-9 / Chapter 3.3.6 --- Al-79wt%Cr --- p.3-10 / Chapter 3.4 --- Reaction mechanisms in the formation of Al-Cr intermetallic compounds --- p.3-12 / Chapter 3.5 --- Summary --- p.3-12 / References --- p.3-14 / Tables and figures --- p.3-15 / Chapter Chapter 4 --- Fabrication of Al-Cr samples by hot-pressing and by arc-melting / Chapter 4.1 --- Introduction --- p.4-1 / Chapter 4.1.1 --- Hot-pressing method --- p.4-1 / Chapter 4.1.2 --- Arc-melting method --- p.4-2 / Chapter 4.2 --- Experiments --- p.4-2 / Chapter 4.3 --- Results and discussions --- p.4-3 / Chapter 4.3.1 --- Hot-pressing method for some specific compositions --- p.4-3 / Chapter 4.3.2 --- Hot-pressing method to produce low Cr content (LC) samples --- p.4-5 / Chapter 4.3.3 --- Effects of hot-pressed time and temperature --- p.4-6 / Chapter 4.3.4 --- Arc-melting method for some specific compositions --- p.4-8 / Chapter 4.3.5 --- Arc-melting method to produce LC samples --- p.4-10 / Chapter 4.4 --- Summary --- p.4-11 / Reference --- p.4-12 / Tables and figures --- p.4-13 / Chapter Chapter 5 --- Thermal expansion coefficients of arc-melted Al-Cr samples / Chapter 5.1 --- Introduction --- p.5-1 / Chapter 5.1.1 --- Thermal expansion --- p.5-1 / Chapter 5.1.2 --- Relations between thermal expansion and structural material --- p.5-1 / Chapter 5.2 --- Experiments --- p.5-2 / Chapter 5.3 --- Results and discussions --- p.5-3 / Chapter 5.3.1 --- TMA results of A1 and Cr --- p.5-3 / Chapter 5.3.2 --- TMA for Al-Cr IMCs --- p.5-3 / Chapter 5.4 --- Summary --- p.5-4 / References --- p.5-6 / Figures --- p.5-7 / Chapter Chapter 6 --- Physical properties of Al-Cr intermetallic compounds / Chapter 6.1 --- Introduction --- p.6-1 / Chapter 6.2 --- Results and discussion --- p.6-1 / Chapter 6.2.1 --- Hot-pressed samples --- p.6-1 / Chapter 6.2.1.1 --- Hot-pressed LC samples --- p.6-2 / Chapter 6.2.1.2 --- Effects of hot-pressing temperature and time --- p.6-3 / Chapter 6.2.2 --- Arc-melted samples --- p.6-4 / Chapter 6.2.3 --- Comparison between the hot-pressed sample and the arc-melted sample --- p.6-6 / Chapter 6.3 --- Summary --- p.6-7 / Tables and figures --- p.6-9 / Chapter Chapter 7 --- Conclusions / Chapter 7.1 --- Summary --- p.7-1 / Chapter 7.2 --- Future works --- p.7-2

Abstract not available

This thesis discusses aspects of a novel solar concentrating photovoltaic / thermal (PV/T) collector that has been designed to produce both electricity and hot water. The motivation for the development of the Combined Heat and Power Solar (CHAPS) collector is twofold: in the short term, to produce photovoltaic power and solar hot water at a cost which is competitive with other renewable energy technologies, and in the longer term, at a cost which is lower than possible with current technologies. To the author’s knowledge, the CHAPS collector is the first PV/T system using a reflective linear concentrator with a concentration ratio in the range 20-40x. The work contained in this thesis is a thorough study of all facets of the CHAPS collector, through a combination of theoretical and experimental investigation. A theoretical discussion of the concept of ‘energy value’ is presented, with the aim of developing methodologies that could be used in optimisation studies to compare the value of electrical and thermal energy. Three approaches are discussed; thermodynamic methods, using second law concepts of energy usefulness; economic valuation of the hot water and electricity through levelised energy costs; and environmental valuation, based on the greenhouse gas emissions associated with the generation of hot water and electricity. It is proposed that the value of electrical energy and thermal energy is best compared using a simple ratio. Experimental measurement of the thermal and electrical efficiency of a CHAPS receiver was carried out for a range of operating temperatures and fluid flow rates. The effectiveness of internal fins incorporated to augment heat transfer was examined. The glass surface temperature was measured using an infrared camera, to assist in the calculation of thermal losses, and to help determine the extent of radiation absorbed in the cover materials. FEA analysis, using the software package Strand7, examines the conductive heat transfer within the receiver body to obtain a temperature profile under operating conditions. Electrical efficiency is not only affected by temperature, but by non-uniformities in the radiation flux profile. Highly non-uniform illumination across the cells was found to reduce the efficiency by about 10% relative. The radiation flux profile longitudinal to the receivers was measured by a custom-built flux scanning device. The results show significant fluctuations in the flux profile and, at worst, the minimum flux intensity is as much as 27% lower than the median. A single cell with low flux intensity limits the current and performance of all cells in series, causing a significant drop in overall output. Therefore, a detailed understanding of the causes of flux non-uniformities is essential for the design of a single-axis tracking PV trough concentrator. Simulation of the flux profile was carried out using the ray tracing software Opticad, and good agreement was achieved between the simulated and measured results. The ray tracing allows the effect of the receiver supports, the gap between mirrors and the mirror shape imperfections to be examined individually. A detailed analytical model simulating the CHAPS collector was developed in the TRNSYS simulation environment. The accuracy of the new component was tested against measured data, with acceptable results. A system model was created to demonstrate how sub components of the collector, such as the insulation thickness and the conductivity of the tape bonding the cells to the receiver, can be examined as part of a long term simulation.

"May 2003" / Includes bibliographical references (leaves 261-270) / xvi, 271, [16] leaves : ill. ; 30 cm. / Title page, contents and abstract only. The complete thesis in print form is available from the University Library. / Thesis (Ph.D.)--University of Adelaide, School of Chemistry and Physics, 2003

A high temperature high vacuum rheometer has been designed, fabricated, and tested for the study of the steady shear viscosity for multicomponent bulk metallic glass forming alloys. This rheometer has an operating range up to 1525 K, rotational frequencies of 9.4*10⁻³-3.7*10¹ radians/s, and a calibrated viscosity range of 9.6*10⁻³ and 1.2*10² Pa*s while maintaining absolute pressures pressure < 1*10⁻⁶ mbar. Zr[subscript 41.2]Ti[subscript 13.8]Cu[subscript 10.0]Ni[subscript 12.5]Be[subscript 22.5] (Vitreloy 1) is reported. The unexpected findings of non-Newtonian behavior above the liquidus temperature were observed. Observations of shear thinning, thixotropic, and viscoelastic behaviors have been made. Our results show that Vitreloy 1 can be modeled as a power law fluid, with a power law exponent of approximately -0.5 for high shear rates. We attribute the non-Newtonian behavior to structural ordering within the melt. The technological and scientific implications for non-Newtonian behavior are discussed. / Graduation date: 2005