Crystallization and multiple melting behavior of bisphenol-A polycarbonate (PC) was investigated using differential scanning calorimetry (DSC) for the monitoring of thermal behavior and atomic force microscopy (AFM) for the morphology study. The exceedingly slow crystallization kinetics of PC and the feasibility of obtaining near monodisperse fractions provide distinct advantages for the elucidation of the effects of crystallization time, temperature, and molar mass on crystallization kinetics. The effects of molar mass on the glass transition temperature (Tg) and heat capacity change at Tg, and the amorphous density of PC were investigated. Similar to many semicrystalline polymers, PC exhibits a multiple melting behavior upon heating. While for each PC sample, the coexistence of low and high temperature endothermic regions in the DSC heating traces is explained by the melting of populations of crystals with different stabilities, melting-recrystallization-remelting effects are observed only for the lowest molar mass samples. The effects of crystallization temperature and molar mass distribution on overall crystallization kinetics were studied for some of the fractions, including the commercial PC-28K (Mw = 28,000 g.mol-1) sample. Regarding the kinetics of secondary crystallization, particular attention was placed on understanding the effects of molar mass, initial degree of crystallinity prior to the secondary crystallization, and secondary crystallization time and temperature. The secondary crystallization of PC follows the same laws discovered in previous studies of PEEK, PET, it-PS and ethylene copolymers, and the results are discussed in the context of a bundle-like secondary crystallization model. During isothermal annealing of semicrystalline PC-28K around the high melting endotherm, a significant increase of melting temperature along with peak broadening with time was observed. Independently, morphological studies using AFM showed that mean lamellar thickness increases with time during isothermal annealing. These results are discussed in light of isothermal thickening of lamellar crystals. Lastly, almost 200 DSC melting traces of varying molar mass PC samples thermally treated under various conditions were analyzed to calculate crystallinity (Xc), rigid fraction (RF), and rigid amorphous fraction (RAF). The correlation between RAF vs Xc, Tg, and Tg broadening are discussed. / Ph. D.

No / Co-crystal screening is routinely undertaken using high-throughput solution growth. We report a low- to medium throughput approach, encompassing both a melt and solution crystallization step as a route to the identification of co-crystals. Prior to solution studies, a melt growth step was included utilizing the Kofler mixed fusion method. This method allowed elucidation of the thermodynamic landscape within the binary phase diagram and was found to increase overall screening efficiency. The pharmaceutically acceptable adduct nicotinamide was selected and screened against a small set of active pharmaceutical ingredients (APIs) (ibuprofen (both the racemic compound (R/S) and S-enantiomer), fenbufen, flurbiprofen (R/S), ketoprofen (R/S), paracetamol, piracetam, and salicylic acid) as part of a larger systematic study of synthon stability. From the screen, three new co-crystal systems have been identified (ibuprofen (R/S and S) and salicylic acid) and their crystal structures determined. Because of poor crystal growth synchrotron radiation was required for structure solution of the S-ibuprofen nicotinamide co-crystal. Two further potential systems have also been discovered (fenbufen and flurbiprofen), but crystals suitable for structure determination have yet to be obtained. A greater ability to control crystallization kinetics is required to yield phase-pure single-crystalline material for full verification of this crystal engineering strategy.

This thesis looks at the study of nanocomposites of Poly(ethylene terephthalate) and organoclays. Two methods of materials blending are investigated for the production of the nanocomposites: solvent blending and melt blending. The main objectives were the investigation of the influence of organoclays and processing conditions on morphological, rheological, mechanical properties, crystal structure and isothermal crystallization kinetics of the nanocomposite and a comparison with unfilled PET. In solvent blending, the use of long sonication time and epoxy led to the formation of a two-dimensional network structure of long, thin particles in a solvent blended PET nanocomposite at low clay loading. The clay network structure seemed not to affect the tensile properties. The long, thin particles were able to be separated and dispersed further by high shear in a twin screw extruder, resulting in a high level of separation and dispersion. The crystallization of the solvent blended nanocomposite was not only influenced by the nanoclay but also by the residual solvent. The extent of clay dispersion did not affect the crystallization of the solvent blended sample. Both solvent blended and melt blended nanocomposites showed that increasing the amount of surfactant improved the degree of nanoclay dispersion in the PET that led to an enhancement in the tensile properties of the nanocomposite compared to the unfilled polymer. The degradation of the organoclay during melt blending did not limit the nanoclay dispersion in the PET. The low thermal stability of the organoclay reduced the strength of the crystalline nanocomposite but it did not affect the strength of the amorphous nanocomposite. In contrast to the solvent blended sample, the extent of clay dispersion influenced the crystallization of the melt blended sample. The poorly dispersed particles were more efficient in nucleating PET crystallization than the well dispersed particles. The crystallization rate of PET increased as the surfactant concentration decreased.

NPLIN was studied in supersaturated solutions (S = 1.06) of potassium chloride (KCl) and bromide (KBr). The fraction of samples nucleated (f) follows a nonlinear dependence on peak power density that approaches f = 1 at higher incident powers. It is shown that a lower threshold power is required for nucleation using 532 nm laser pulses than at 1064 nm, and that a higher fraction of samples nucleate when exposed to 532 nm pulses at a given laser power. Comparison with KCl shows higher fractions of KBr samples nucleate with lower threshold values at both wavelengths. Samples of KCl of equal supersaturation at two different temperatures (23 and 33 °C) exposed to 1064 nm pulses show that those at 33 °C are significantly more labile to nucleation. The ratio of samples nucleated at 33 °C compared to those at 23 °C was 2.11 ± 0.47. A classical nucleation model based on activation of subcritical solute clusters accounts remarkably well for the experimental data and provides phenomological values of the crystal–solution interfacial tension (γ) at 23 °C for KCl and KBr of 5.283 and 4.817 mJ m-2. At 33 °C, the model yields a best-fit value of γ = 5.429 mJ m-2 for KCl. As an extension of this work the use of an evanescent wave (ew) generated by total internal reflection was investigated as a method to cause nucleation in supersaturated KCl solution. Evanescent wave NPLIN (ew-NPLIN) was shown to cause nucleation. The results showed a higher laser-power threshold required for nucleation and sample lability greater than that of bulk NPLIN. In a second approach to understanding NPLIN, the structures of concentrated solutions were probed by a series of laser scattering experiments. Evidence showing populations of particles in solution was provided by Rayleigh laser scattering (RLS) experiments. Scattering in solutions prepared to be nearly saturated (S = 0.95) was observed using a low magnification (×10) microscope objective; almost all solutions showed the presence of scattering objects moving freely in solution. For those that showed no particles, it was noted that the solutions were typically of higher solute concentration (> 11 mol% solute). Ammonium nitrate solution showed no particles using ×10 magnification, however particles were identified when higher magnification was used (×50 and ×100). Video footage of the Rayleigh scattering observed in aqueous solutions of glycine, urea and ammonium nitrate obtained using ×50 magnification were analysed using a custom nanoparticle tracking software. The results showed a population of particles in aqueous urea and glycine solutions with particle concentrations of the order 108 particles cm-3 and mean hydrodynamic diameter of approximately 267 ± 1 and 173 ± 2 nm respectively. Not enough particles were identified in ammonium nitrate solution to complete the tracking analysis; however a fluctuating background scatter suggested a population of particles with sizes below the limit of resolution of the optical system. Using aqueous urea solution as a model system the structure of the particles identified in solution was investigated using scanning microscopy. The second-harmonic scattering (SHS) signal measured in concentrated aqueous urea solution was measured as a function of solution concentration (C) over a range of saturation conditions from undersaturated (S = 0.15) to supersaturated (S = 1.86). The results show a non-linear increase in SHS signal with local maxima near S = 0.95 and 1.75 suggesting a change in solution structure near these points. Rayleigh scattering images indicate the presence of particles in nearly saturated (S = 0.95) urea solutions. Time-dependent SHS measurements indicate that signals originate from individual events encountered during scanning of the sample through the focal volume of the probe laser, consistent with second harmonic generation (SHG) from particles. SHG from aqueous dispersions of barium titanate (BaTiO3) nanoparticles with diameters < 200 nm, showed signals ~20 times larger than urea solutions. The results suggest the existence of a population of semi-ordered clusters of urea that changes with solution concentration.

by Yang Hua. / "August 1999." / Thesis (Ph.D.)--Chinese University of Hong Kong, 1999. / Includes bibliographical references. / Electronic reproduction. Hong Kong : Chinese University of Hong Kong, [2012] System requirements: Adobe Acrobat Reader. Available via World Wide Web. / Mode of access: World Wide Web. / Abstracts in English and Chinese. / by Yang Hua.

Ngai Hau Wai. / Thesis (M.Phil.)--Chinese University of Hong Kong, 1998. / Includes bibliographical references. / Text in English; abstract also in Chinese. / Ngai Hau Wai. / Acknowledgements --- p.ii / Abstract --- p.iii / Chapter Chapter 1: --- Introduction --- p.1 / Chapter 1.1 --- History of nanomaterials --- p.1 / Chapter 1.2 --- Application and properties of nanomaterials --- p.2 / Chapter 1.3 --- Thermodynamic of a binary system --- p.4 / Chapter 1.4 --- Nucleation and growth --- p.5 / Chapter 1.5 --- Spinodal decomposition --- p.7 / References --- p.10 / Figures --- p.11 / Chapter Chapter 2: --- Experimental setup and techniques --- p.21 / Chapter 2.1 --- How to achieve high undercooling? --- p.21 / Chapter 2.2 --- Preliminary steps --- p.22 / Chapter 2.2.1 --- Preparation of dehydrated B203 --- p.22 / Chapter 2.2.2 --- Preparation of the apparatus --- p.23 / Chapter 2.2.3 --- Preparation of Ni2P --- p.23 / Chapter 2.2.4 --- Alloying --- p.23 / Chapter 2.3 --- Experiment --- p.24 / Chapter 2.3.1 --- Preparation of pure glass --- p.24 / Chapter 2.3.2 --- Anneal the glass pieces at different temperature for 30 minutes… --- p.24 / Chapter 2.4 --- Investigation --- p.25 / Chapter 2.4.1 --- Thermal Properties --- p.25 / Chapter 2.4.2 --- TEM observation --- p.25 / References --- p.27 / Figures --- p.28 / Chapter Chapter 3: --- Crystallization kinetics of amorphous nanostructured materials --- p.32 / Abstract --- p.32 / Chapter 3.1 --- Introduction --- p.33 / Chapter 3.2 --- Experimental --- p.34 / Chapter 3.3 --- Results and Discussion --- p.35 / References --- p.41 / Figures --- p.42

by Leung Ching Chuen. / Thesis (M.Phil.)--Chinese University of Hong Kong, 1998. / Includes bibliographical references (leaf 47). / Text in English; abstract also in Chinese. / by Leung Ching Chuen. / Acknowledgments --- p.ii / Abstract --- p.iii / Chapter Chapter 1 --- Introduction --- p.1 / Chapter 1.1 --- Expansion of the Mesoscopic World --- p.2 / Chapter 1.2 --- Nanostructured Materials --- p.3 / Chapter 1.3 --- A New Age --- p.4 / Chapter 1.4 --- """Flaws"" of the New Age" --- p.5 / Chapter 1.5 --- Phase Transformation --- p.7 / Chapter 1.6 --- Nucleation and Growth --- p.8 / Chapter 1.7 --- Spinodal Decomposition --- p.11 / Chapter 1.8 --- Morphology Change during Spinodal Decomposition --- p.13 / References --- p.16 / Figures --- p.17 / Chapter Chapter 2 --- Experiment --- p.25 / Chapter 2.1 --- Experimental Preparations --- p.27 / Chapter 2.1.1 --- Fused Silica Tube Preparation --- p.27 / Chapter 2.1.2 --- Alloying --- p.27 / Chapter 2.2 --- Experimental Procedures --- p.28 / Chapter 2.2.1 --- Fluxing --- p.28 / Chapter 2.2.2 --- Undercooling --- p.29 / Chapter 2.3 --- Sample Analysis --- p.30 / Chapter 2.3.1 --- Surface Analysis --- p.30 / Chapter 2.3.2 --- Differential Scanning Calorimetry (DSC) --- p.30 / Chapter 2.3.3 --- Hardness Testing --- p.31 / Chapter 2.3.4 --- Optical Microscopy --- p.32 / Chapter 2.3.5 --- Scanning Electron Microscopy (SEM) --- p.32 / Chapter 2.3.6 --- Transmission Electron Microscopy (TEM) --- p.32 / Chapter 2.3.7 --- X-ray Powder Diffraction (XPD) --- p.33 / References --- p.34 / Figures --- p.35 / Chapter Chapter 3 --- Mechanism of Bulk Nanostructured Material Formation by Metastable Liquid State Spinodal Decomposition --- p.38 / Abstract --- p.39 / References --- p.47 / Figures --- p.48 / Chapter Chapter 4 --- Formation of Amorphous Nanostructured Material --- p.57 / Abstract --- p.58 / References --- p.66 / Figures --- p.67 / Chapter Chapter 5 --- Crystallization Kinetics of Amorphoous Nanostructured Alloy --- p.75 / Abstract --- p.76 / References --- p.85 / Figures --- p.86 / Chapter Chapter 6 --- Conclusion --- p.101

這篇論文研究了幾種基於聚二甲基硅氧烷（PDMS）的微流控芯片，及其對於酶反應和蛋白質結晶的應用。 / 本論文分為兩部份。首先，論文第一部份介紹了兩種微流控芯片。利用到PDMS透氣的性質，第一種微流控芯片是一種基於脫氣PDMS的納升液體進液系統。在第一種微流控芯片的基礎上，我們引進一種可由普通注射器控制的氣閥控制系統，可對反應液體的分配和混合進行更方便和精確的操作。兩種芯片均成功應用於酶反應動力學的測定。在一次實驗中，只需要3~5微升的反應物就可以得到鹼性磷酸酶（alkaline phosphatase）的Michaelis-Menten動力學。 / 論文第二部份研究了“體積效“應對於蛋白質結晶的影響。首先，基於微孔的微流控芯片的蛋白質結晶篩選實驗揭示了在小體積（納升）下，蛋白質的結晶條件比在大體積（微升）下更多。在液滴里的蛋白質結晶實驗結果說明大體積的蛋白質液滴結晶速度更快。最後，蛋白質結晶實驗成功在雙乳液（double emulsion）的內核中進行。 / This thesis describes the design and development of micro dispensing systems for enzyme assay and for protein crystallization. The micro dispensing systems were fabricated by the soft-lithography method with the widely used material poly(dimethylsiloxane) (PDMS), which is gas and water permeable elastomer. / This thesis contains two major parts. In the first part, enzyme assay was performed in two micro dispensing systems, one based on microwells and the other based on pneumatic valves. The complete Michaelis-Menten kinetics measurement of the alkaline phosphatase (AP) with different fluorescein diphosphate (FDP) was achieved in one chip for each system using the fluorescence detection. These micro dispensing systems’ fabrication and operation were simple, and the total sample consumption was about 3~5 μL. / The second part reports the study of the volume effect on protein crystallization. Three micro dispensing systems, the microwell-based, droplet-based and double emulsion-based systems, were developed to perform the protein crystallization. Lysozyme and thaumatin were chosen as the model proteins. First, the protein crystallization screening experiments showed that protein crystallized in more precipitant conditions in the microchip than in conventional microbatch system. Second, the protein crystallization results carried out in droplets showed that protein crystallized faster in larger droplets. Finally, the protein crystallization in double emulsions was demonstrated. / Detailed summary in vernacular field only. / Detailed summary in vernacular field only. / Detailed summary in vernacular field only. / Zhou, Xiaohu. / Thesis (Ph.D.)--Chinese University of Hong Kong, 2012. / Includes bibliographical references (leaves 87-91). / Electronic reproduction. Hong Kong : Chinese University of Hong Kong, [2012] System requirements: Adobe Acrobat Reader. Available via World Wide Web. / Abstract also in Chinese. / Abstract --- p.i / 摘要 --- p.iii / Acknowledgements --- p.iv / Table of Contents --- p.vi / List of figures --- p.viii / Chapter Chapter 1 --- Introduction to microfluidics --- p.1 / Chapter 1.1 --- Fabrication of microfluidic devices --- p.2 / Chapter 1.1.1 --- PDMS-based microfluidic device --- p.2 / Chapter 1.1.2 --- PMMA microfluidic device --- p.6 / Chapter 1.1.3 --- Assembly of the microfluidic device --- p.8 / Chapter 1.2 --- Degassed PDMS pumping method --- p.9 / Chapter 1.3 --- Droplet-based microfluidics --- p.13 / Chapter 1.4 --- Thesis organization --- p.16 / Chapter Chapter 2 --- Micro dispensing systems for enzyme assay --- p.17 / Chapter 2.1 --- Introduction to enzyme assay --- p.17 / Chapter 2.1.1 --- Introduction to micro platforms for enzyme assay --- p.17 / Chapter 2.1.2 --- Introduction to enzyme kinetics and Michaelis-Menten kinetics --- p.21 / Chapter 2.2 --- Experimental --- p.26 / Chapter 2.2.1 --- Design of the micro dispensing systems --- p.26 / Chapter 2.2.2 --- Fabrication of the microfluidic devices --- p.30 / Chapter 2.2.3 --- Reagents and operation --- p.32 / Chapter 2.3 --- Results and discussion --- p.32 / Chapter 2.3.1 --- Microwell-based dispensing system --- p.32 / Chapter 2.3.2 --- Micro dispensing system based on pneumatic valves --- p.40 / Chapter 2.4 --- Conclusions --- p.45 / Chapter Chapter 3 --- Micro dispensing systems for protein crystallization --- p.47 / Chapter 3.1 --- Introduction to protein crystallization --- p.47 / Chapter 3.1.1 --- Principle of protein crystallization --- p.49 / Chapter 3.1.2 --- From macrofluidics to microfluidics --- p.51 / Chapter 3.2 --- Experimental --- p.56 / Chapter 3.2.1 --- Design of the micro dispensing systems --- p.56 / Chapter 3.2.2 --- Fabrication of the microfluidic devices --- p.58 / Chapter 3.2.3 --- Reagents and operation --- p.60 / Chapter 3.2.4 --- Layer-by-layer modification --- p.61 / Chapter 3.3 --- Results and discussion --- p.65 / Chapter 3.3.1 --- Demonstration of the micro dispensing systems --- p.65 / Chapter 3.3.2 --- Protein crystallization screening results --- p.69 / Chapter 3.3.3 --- Protein crystallization in droplets --- p.73 / Chapter 3.3.4 --- Protein crystallization in w/o/w double emulsions --- p.77 / Chapter 3.4 --- Conclusions --- p.80 / Appendix --- p.82 / References --- p.87

by Leung Kwok Kuen. / Thesis (Ph.D.)--Chinese University of Hong Kong, 1997. / Electronic reproduction. Hong Kong : Chinese University of Hong Kong, [2012] System requirements: Adobe Acrobat Reader. Available via World Wide Web. / Mode of access: World Wide Web. / by Leung Kwok Kuen.

Fe-B熔體可鑄造成網絡狀合金的微觀結構。研究顯示，熔融狀態的Fe₈₄B₁₆在275 K 過冷時將發生形態轉變。實驗結果指出熔融狀態的Fe-B合金存在一亞穏液態互溶區。該互溶區範圍為Fe₈₄B₁₄.到Fe₈₂B₁₈.。Fe-B網絡狀合金的微觀結構，由一個易碎的Fe₃B子網絡和一個具延展性的αFe子網絡組成。因此Fe-B網絡狀合金擁有具吸引性的物理性能。 / 由於Fe₈₄B₁₆網絡狀合金並不存在任何微孔，因此我們可推斷合金在結晶的過程中，兩個子網絡的固體/液體界面將一起生長。而且，在固體/液體界面前並不具有硼原子的濃度梯度。因此我們提出了一個生長模型來分析Fe-B網絡狀合金來自掃瞄電子顯微鏡和透射電子顯微鏡的檢測結果。Fe-B網絡狀合金的結晶動力學和微觀結構均得到解釋。研究顯示，合金中的兩個子網絡均擁有特定的生長方向，並且以樹枝晶的方式來生長。 / Molten Fe₁₀₀-{U+2093}B{U+2093} melts, where x = 14 to 18, can be cast into ingots of network morphology. It was found that there is a morphological transition in molten Fe₈₄B₁₆.with undercooling of 275 K. The experimental results indicate that there is a metastable liquid miscibility gap in undercooled Fe-B melts. The network morphology consists of two interconnected subnetworks, which are αFe subnetwork and Fe₃B subnetwork respectively. The Fe-B network alloys have attractive mechanical properties. / As micropore does not exist in the Fe₈₄B₁₆ network ingot, it is proposed that the solid/liquid interfaces of the two subnetworks advance together during solidification. In addition, there is no composition gradient of boron atoms at the growth front. A growth model is proposed to explain the results by scanning electron microscopy and transmission electron microscopy. It was found that there is special crystallinity in Fe₈₄B₁₆ network ingots. / Detailed summary in vernacular field only. / Detailed summary in vernacular field only. / Wong, Tak Cheung = 鐵硼網狀合金的形成和結晶動力學 / 黃德彰. / Thesis (M.Phil.)--Chinese University of Hong Kong, 2012. / Includes bibliographical references. / Abstracts also in Chinese. / Wong, Tak Cheung = Tie peng wang zhuang he jin de xing cheng he jie jing dong li xue / Huang Dezhang. / Abstract --- p.ii / Acknowledge --- p.iv / List of Table --- p.vii / List of Figures --- p.viii / Chapter Chapter 1 --- Introduction --- p.1 / Chapter 1.1 --- Phase diagram --- p.1 / Chapter 1.1.1 --- Undercooling --- p.1 / Chapter 1.2 --- Nucleation and Growth --- p.2 / Chapter 1.2.1 --- Homogeneous Nucleation --- p.3 / Chapter 1.2.2 --- Heterogeneous Nucleation --- p.3 / Chapter 1.2.3 --- Growth --- p.6 / Chapter 1.2.3.1 --- Growth of Pure Metal --- p.6 / Chapter 1.2.3.2 --- Solid/Liquid interface stability --- p.7 / Chapter 1.2.3.3 --- Solidification of Single Phase Binary Alloys --- p.8 / Chapter 1.2.3.3.1 --- Equilibrium Solidification --- p.8 / Chapter 1.2.3.3.2 --- Non-Equilibrium Solidification --- p.8 / Chapter 1.2.3.3.3 --- Morphology Change --- p.9 / Chapter 1.2.3.4 --- Solidification of the Binary Eutectic Alloy --- p.10 / Chapter 1.2.3.4.1 --- Growth of Lamellar Eutectics --- p.10 / Chapter 1.2.3.4.2 --- Off-Eutectic Alloys --- p.11 / Chapter 1.3 --- Binary Systems with a Solid Miscibility Gap --- p.11 / Chapter 1.4 --- Phase Separation Mechanisms in a Solid Miscibility Gap --- p.12 / Chapter 1.4.1 --- Nucleation and Growth --- p.12 / Chapter 1.4.2 --- Spinodal Decomposition --- p.13 / Chapter 1.4.4.1 --- The initiation of Spinodal Decomposition --- p.13 / Chapter 1.4.4.2 --- Diffusion Equation of Spinodal Decomposition --- p.14 / Chapter 1.4.4.3 --- Solution to the Modified Diffusion Equation --- p.17 / Figures --- p.18 / References / Chapter Chapter 2 --- Experimental --- p.29 / Chapter 2.1 --- Preparation of fused silica tube --- p.29 / Chapter 2.2 --- Alloying and fluxing --- p.29 / Chapter 2.3 --- Undercooling --- p.30 / Chapter 2.4 --- Sample Preparation --- p.31 / Chapter 2.4.1 --- Cutting, Grinding and Polishing --- p.31 / Chapter 2.4.2 --- Sample preparation for Scanning Electron Microscopy (SEM) --- p.32 / Chapter 2.4.3 --- Sample preparation for Transmission Electron Microscopy (TEM) --- p.32 / Chapter 2.5 --- Microhardness Test --- p.33 / Chapter 2.6 --- Compression Test --- p.33 / Chapter 2.7 --- Microstructure Analysis --- p.34 / Chapter 2.7.1 --- Scanning Electron Microscopy Analysis --- p.34 / Chapter 2.7.2 --- Transmission Electron Microscopy Analysis --- p.34 / Chapter 2.7.3 --- Indexing Diffraction Patterns --- p.34 / Figures --- p.36 / Chapter Chapter 3 --- Formation of Fe-B network alloys --- p.38 / Chapter 3.1 --- Abstract --- p.38 / Chapter 3.2 --- Introduction --- p.39 / Chapter 3.3 --- Experimental --- p.40 / Chapter 3.4 --- Results --- p.42 / Chapter 3.5 --- Discussion --- p.47 / Chapter 3.6 --- Conclusions --- p.48 / Figures --- p.50 / References --- p.69 / Chapter Chapter 4 --- SEM and TEM studies of Fe84B16 70 alloys of network morphology --- p.70 / Chapter 4.1 --- Abstract --- p.70 / Chapter 4.2 --- Introduction --- p.71 / Chapter 4.3 --- Background --- p.71 / Chapter 4.4 --- Experimental --- p.73 / Chapter 4.5 --- Results --- p.74 / Chapter 4.6 --- Discussions --- p.81 / Chapter 4.7 --- Conclusions --- p.85 / Figures --- p.87 / References --- p.106