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Library of Congress Cataloging-in-Publication Data is available.
ISBN: 9781119494218
ISSN: 1042-1122

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CONTENTS

PREFACE

Multiscale Modeling and Simulation

D⁰ FERROMAGNETISM OF SIC CERAMICS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGMENTS
7. REFERENCES

Innovative Processing and Manufacturing

CONTROLLING FACTORS FOR CREATING DENSE SiC-POLYCRYSTALLINE FIBER
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES
ECO-FRIENDLY SYNTHESIS OF GRAPHENE USING HIGH PRESSURE AIRLESS SPRAY SYSTEM
1. ABSTRACT
2. 1. INTRODUCTION
3. 2. PROCESS
4. 3. RESULTS
5. 4. DISCUSSION
6. 5. CONCLUSION
7. 6. REFERENCES
EFFECT OF ION IMPLANTATION ON A PRECURSOR POLYMER FOR SYNTHESIS OF CARBON MATERIAL WITH CATALYTIC PERFORMANCE
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
MICROSTRUCTURE AND GRAIN SIZE DISTRIBUTIONS IN MAGNESIA-ALUMINA SPINEL CERAMICS PREPARED BY SPARK PLASMA SINTERING
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL DETAILS, MEASUREMENT PROCEDURES, USEFUL RELATIONS
4. RESULTS AND DISCUSSION
5. SUMMARY AND CONCLUSION
6. ACKNOWLEDGEMENT
7. REFERENCES
MICROSTRUCTURE CHARACTERIZATION OF POROUS CERAMICS VIA MINKOWSKI FUNCTIONALS
1. ABSTRACT
2. INTRODUCTION
3. THEORETICAL BACKGROUND AND PRACTICAL RECIPES
4. CASE STUDIES: MICROSTRUCTURE CHARACTERIZATION OF CERAMIC FOAMS
5. CONCLUSION
6. ACKNOWLEDGEMENT
7. REFERENCES
NUMERICAL MODELING OF ELASTIC MODULUS AND CONDUCTIVITY OF POROUS ALUMINA – EFFECTS OF PORE SHAPE, PORE SIZE DISTRIBUTION AND PORE DISTANCE
1. ABSTRACT
2. INTRODUCTION
3. GENERATION OF DIGITAL MICROSTRUCTURES AND CALCULATION OF EFFECTIVE PROPERTIES
4. INFLUENCE OF THE PORE SHAPE AND PORE SPACE CONNECTIVITY (TOPOLOGY) ON THE EFFECTIVE PROPERTIES
5. INFLUENCE OF THE PORE SIZE DISTRIBUTION AND MINIMUM PORE DISTANCE ON THE EFFECTIVE PROPERTIES
6. CONCLUSION
7. ACKNOWLEDGEMENT
8. REFERENCES
EXPERIMENTAL INVESTIGATION AND ANALYSIS OF MECHANICAL PROPERTIES OF THREE-DIMENSIONALLY NETWORKED POROUS CARBON MATERIAL
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL PROCEDURE
4. RESULTS AND DISCUSSION
5. CONCLUDING REMARKS
6. REFERENCES

Nanotechnology and Structural Ceramics

DEVELOPMENT OF MINIATURE GENERATOR COMBINED WITH MAGNETIC CERAMIC MATERIAL AND SILICON MICRO AIR TURBINE
1. ABSTRACT
2. INTRODUCTION
3. DESIGN OF AIR TURBINE GENERATOR WITH FLUID-DYNAMIC BEARING SYSTEM
4. DESIGN OF BALL BEARING SYSTEM AIR TURBINE GENERATOR
5. RESULTS AND DISCUSSION
6. CONCLUSION
7. ACKNOWLEDGMENT
8. REFERENCES
TEMPERATURE DEPENDENCE OF YOUNG’S MODULUS OF SILICATE CERAMICS FROM THE MAGNESIA–ALUMINA–SILICA SYSTEM
1. ABSTRACT
2. INTRODUCTION
3. THEORETICAL
4. EXPERIMENTAL
5. RESULTS AND DISCUSSION
6. CONCLUSION
7. ACKNOWLEDGEMENT
8. REFERENCES
SINTERING, STRUCTURE AND PROPERTIES OF AlB12–BASED CERAMICS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
HIGH DIELECTRIC STRENGTH CERAMIC FOR POWER TUBES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES
MICROSTRUCTURAL AND MECHANICAL CHARACTERIZATION OF DAMAGE TOLERANT SIC/SICN CERAMIC MATRIX COMPOSITES MANUFACTURED VIA PIP PROCESS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
CRYSTAL STRUCTURE OF THE DEFECT PYROCHLORE POTASSIUM TANTALATE ON ION-EXCHANGING DIPPING IN SODIUM AQUEOUS SOLUTION BY RIETVELD ANALYSIS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL METHODS
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. ACKNOWLEDGEMENT
7. REFERENCES
PREPARATION AND STRUCTURE OF GEOPOLYMER-BASED ALKALI-ACTIVATED CIRCULATING FUILDIZED BED ASH COMPOSITE FOR REMOVING Ni²⁺ FROM WASTEWATER
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGMENTS
7. REFERENCES

Multifunctional Materials and Systems

DIELECTRIC PROPERTIES AND RESOURCE CRITICALITY ASPECTS OF HEXAGONAL MANGANITE
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. ACKNOWLEDGEMENTS
7. REFERENCES
CATALYTIC ACTIVITY OF LIQUID-PHASE REACTION OVER PEROVSKITE-TYPE OXIDE CATALYST SYNTHESIZED FROM HETERONUCLEAR METAL CYANO COMPLEX PRECURSOR
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. CATALYTIC REACTION IN LIQUID PHASE
5. RESULTS AND DISCUSSION
6. KNÖEVENAGEL CONDENSATION
7. CRYSTALLINITY OF PEROVSKITE-TYPE OXIDE SYNTHSIZED BY THERMAL DECOMPOSITION OF COORDINATION POLYMER PRECURSOR
8. CONCLUSIONS
9. ACKNOWLEDGEMENTS
10. REFERENCES
DEVELOPMENT OF TUNABLE DEVICES USING BARIUM STRONTIUM TITANATE THIN FILMS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. APPLICATIONS
6. CONCLUSIONS
7. REFERENCES
DIELECTRIC PROPERTIES OF CONFINED IONIC LIQUIDS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. ACKNOWLEDGEMENTS
7. REFERENCES
LARGE FORMAT LI CO-DOPED NAI:TL (NAIL^TM) SCINTILLATION DETECTOR FOR GAMMA-RAY AND NEUTRON DUAL DETECTION
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. DISCUSSION AND CONCLUSIONS
5. REFERENCES
ANNEALING INDUCED STRUCTURAL PHASE CHANGE OF HEXAGONAL-LuFeO₃ THIN FILMS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
PROCESSING AND CHARACTERIZATION OF ZINC SULFIDE AND CALCIUM FLUORIDE COMPOSITE CERAMICS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES

Ceramics for Energy and Environment

THERMOELECTROCHEMICAL CELLS WITH MOLTEN CARBONATE ELECTROLYTES AND GAS ELECTRODES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES
CATALYTIC SO₃ DECOMPOSITION ACTIVITY AND STABILITY OF SUPPORTED MOLTEN VANADATE CATALYSTS FOR SOLAR THERMOCHEMICAL WATER SPLITTING CYCLES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
RECENT DEVELOPMENTS ON ISOL TARGETS FOR THE SPES PROJECT FOR NUCLEAR PHYSICS AND APPLICATIONS
1. ABSTRACT
2. INTRODUCTION
3. THE SPES TARGET
4. MATERIALS FOR THE SPES TARGET
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
NUCLEAR FUEL MODELLING AND PERSPECTIVES ON CANADIAN EFFORTS IN FUEL DEVELOPMENT
1. ABSTRACT
2. INTRODUCTION
3. NUCLEAR FUEL MODELLING
4. NUCLEAR FUEL EXPERIMENTS
5. PERSPECTIVES ON CANADIAN EFFORTS IN FUEL DEVELOPMENT
6. CONCLUSION
7. ACKNOWLEDGEMENTS
8. REFERENCES
LOW-COST PREPARATION METHOD FOR ANTI-DIRT COATING ON CONCRETE BLOCK USING TITANIUM OXIDE PHOTOCATALYTIC POWDER
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES
DEVELOPMENT OF DIELECTRIC MATERIALS BASED ON MULTILAYER CERAMIC CAPACITORS FOR HIGH TEMPERATURE APPLICATIONS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. REFERENCES
TOWARDS HIGH ENERGY DENSITY GLASS CAPACITORS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL METHODS
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES

Ceramics in Biology, Medicine and Human Health

DESIGN OF EXPERIMENT OPTIMIZATION OF ARTIFICIAL BONE CONSTRUCT FABRICATION VIA DIRECT INK WRITING OF HYDROXYAPATITE
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES
RECENT TOPICS IN THE FIELD OF FERROELECTRIC MATERIALS FOR BME-MLCCs
1. ABSTRACT
2. INTRODUCTION
3. DISCONTINUOUS PROGRESS IN MLCC TECHNOLOGY
4. RECENT TOPICS IN THE FIELD OF DIELECTRIC MATERIALS
5. TEMPERATURE STABLE DIELECTRICS FOR HIGH TEMPERATURE APPLICATIONS
6. SUMMARY
7. REFERENCES

Young Investigator Forum: Design and Application of Next Generation Multifunctional Materials

HIGH TEMPERATURE DURABILITY OF OXIDE-OXIDE CERAMIC MATRIX COMPOSITES EXPOSED TO ENGINE RELEVANT CONDITIONS
1. ABSTRACT
2. INTRODUCTION
3. METHODOLOGY
4. RESULTS & DISCUSSIONS
5. CONCLUSIONS
6. ACKNOWLEDGEMENTS
7. REFERENCES

END USER LICENSE AGREEMENT

List of Tables

Chapter 2

Table 1.

Chapter 3

Table 1:

Chapter 5

Table 1.
Table 2.
Table 3.
Table 4.

Chapter 6

Table 1.

Chapter 7

Table 1.
Table 2.
Table 3.
Table 4.

Chapter 8

Table 1.

Chapter 9

Table 1.
Table 2.

Chapter 10

Table 1.
Table 2.
Table 3.
Table 4.
Table 5.
Table 6.
Table 7.

Chapter 11

Table I.
Table 2.
Table 3.

Chapter 12

Table 1.

Chapter 15

Table 1:

Chapter 16

Table 1:

Chapter 20

Table I.

Chapter 27

Table 1.
Table 2.
Table 3.
Table 4.

Chapter 30

Table I.
Table II.
Table III.

List of Illustrations

Chapter 1

Fig. 1 Band structure calculation of 6H-SiC
Fig. 2 The electron spin density of the states of 6H-SiC
Fig. 3 XRD pattern of Al:SiC powder after calcination at 2000^oC
Fig. 4 Sketch of defects in the supercell of 3 × 3 × 1 Al:SiC and its electron spin density of the states, in which one Si (yellow ball) atom is replaced with one Al (red ball) atom, one Si atom is replaced with Vacancy, and all C (gray ball) atoms remain in the same in defects.
Fig. 5 The hysteresis loops for different Al doping SiC ceramics
Fig. 6 SiC slip with and without magnet oriented in magnetic field (6T)
Fig. 7 Magnetic force microscopy images of d⁰ ferromagnetic SiC ceramics (a, b, c) and pure SiC ceramics (d, e, f). (a,d) surface morphology, (b, e) magnetic domain, (c. f) magnetic domain rotating 45o in the base of b).

Chapter 2

Fig. 1 The production scheme of the SiC-polycrystalline fiber using a raw Si-Al-C-O fiber
Fig. 2 Changes in the surface structure after immediate heating up to various temperatures This type of surface grain growth was caused by the reaction between SiO gas and diffused carbon according to the following reaction.
Fig. 3 The cross-section of the undesirable fiber containing lots of residual carbon
Fig. 4 A general process using self-forming and self-consuming “Just-in-time Reactor” system
Fig. 5 Detailed process using the “Just-in-time Reactor” system
Fig. 6 Auger electron spectroscopy (AES) depth profiles of the pre-oxidized raw fiber
Fig. 7 TEM image of the surface region of the pre-oxidized raw fiber after immediate heat-treatment at 1410^oC in argon atmosphere.
Fig. 8 TEM image of the surface region of the pre-oxidized raw fiber after immediate heat-treatment at 1450^oC in argon atmosphere.
Fig. 9 Cross-section of the SiC-polycrystalline fiber synthesized by the use of pre-oxidized Si-Al-C-O fiber along with the comparative result using non-oxidized fiber.

Chapter 3

Figure 1: Exfoliation using air pressure
Figure 2: Schematic diagram of atomization process
Figure 4: XRD plots of graphite soaked with different concentrations
Figure 5: XRD plots of graphite soaked in 1% salt at different time intervals
Figure 6: Raman Spectra of exfoliated solution at different pressures
Figure 7: High Pressure exfoliated Graphene characterisation a) TEM image of a graphene flake b) Electron diffraction pattern of the produced graphene showing clearly six membered ring. (c) HR-TEM image of graphene and corresponding FFT image (inset). (d) Raman spectra of the graphene sample

Chapter 4

Figure 1. Isolation process of N ion-irradiated part of phenol resin.
Figure 2. FT-IR spectra of N⁺ ion irradiated phenol resin.
Figure 3. XPS N 1s spectra of N⁺ ion irradiated phenol resin.
Figure 4. Raman spectra of N⁺ ion irradiated phenol resin after pyrolysis at 800 °C.
Figure 5. XPS spectra of N⁺ ion irradiated phenol resin after pyrolysis at 800°C.
Figure 6. Results of ORR activity evaluation for obtained N-doped carbon material.

Chapter 5

Figure 1. Particle size distribution of the MAS powder measured via laser diffraction (cumulative curves full and frequency curves dashed); left hand side curves: primary particles and agglomerates, right hand side curves: only primary particles.
Figure 2. Grain microstructure of transparent MAS ceramics prepared by SPS (A – top left, B – top right, C – bottom left, D – bottom right); SEM micrographs of thermally etched planar sections.
Figure 3. Grain size distributions of four MAS ceramic samples prepared by SPS (A – top left, B– top right, C – bottom left, D – bottom right); original data (data points) and transformed results (Saltykov – solid curve, Cruz-Orive – dashed curve, Woodhead – dotted curve).
Figure 4. Grain size distributions of four MAS ceramic samples prepared by SPS (A – top left, B– top right, C – bottom left, D – bottom right), fitted using the four-parameter fit relation.

Chapter 6

Figure 1. First section plane (slice no. 1 of 100) of porous mullite-based ceramic foam; grey-scale image (left hand side) and binarized image (right hand side), resolution (voxel and pixel edge length) 4.9 μm.
Figure 2. Second section plane (slice no. 10 of 100, binarized image, left hand side) of porous mullite-based ceramic foam in distance 44.1 μm (9 x 4.9 μm) from the first (right hand side of Figure 1) and semitransparent overlay of the two section planes (right hand side); mullitealumina composite foam prepared with wheat flour.
Figure 3. Automatic object count (using NIS Elements, Laboratory Imaging, Czech Republic) on the first section plane (slice no. 1, left hand side), on the union of the first and second section plane (slices no. 1 and 10, middle) and on the intersection of the first and second section plane (slices no. 1 and 10, right hand side); mullite-alumina composite foam prepared with wheat flour.
Figure 4. First section plane (slice no. 1 of 100) of porous mullite-based ceramic foam; grey-scale image (left hand side) and binarized image (right hand side), resolution (voxel and pixel edge length) 4.9 μm; alumina foam prepared by biological foaming with yeast.
Figure 5. Automatic object count on the first and second section plane (left hand side), on the union of the first and second section plane (middle) and on the intersection of the first and second section plane (right hand side); alumina foam prepared by biological foaming with yeast.

Chapter 7

Figure 1. Porosity dependence of the effective thermal conductivity of porous alumina ceramics with different microstructures (convex and concave pores, the latter being voids between convex grains, isolated or overlapping, based on different arrangements of pores or grains: simple cubic / SC, body-centered cubic / BCC, face-centered cubic / FCC, maximally random jammed / MRJ).
Figure 2. Porosity dependence of the effective Young’s modulus of porous alumina ceramics with different microstructures (convex and concave pores, the latter being voids between convex grains, isolated or overlapping, based on different arrangements of pores or grains: simple cubic / SC, body-centered cubic / BCC, face-centered cubic / FCC, maximally random jammed / MRJ).
Figure 3. Porosity dependence of the effective thermal conductivity of porous alumina ceramics with different microstructures: alumina foams (periodic Kelvin-cell foams and random foams, either closed-cell or open-cell) and alumina ceramics with anisometric (spheroidal) pores with aspect ratio 10 (prolate) and 0.1 (oblate), either isolated or overlapping.
Figure 4. Porosity dependence of the effective Young’s modulus of porous alumina ceramics with different microstructures: alumina foams (periodic Kelvin-cell foams and random foams, either closed-cell or open-cell) and alumina ceramics with anisometric (spheroidal) pores with aspect ratio 10 (prolate) and 0.1 (oblate), either isolated or overlapping.
Figure 5. Examples of digital random microstructures with bidisperse pore size distributions consisting of 50 vol.% large and 50 vol.% small pores with size ratios 2:1 – isolated (A, B), 5:1 – isolated (C, D), 10:1 – isolated (E, F) and 10:1 overlapping (G, H); ϕ = porosity.
Figure 6. Examples of digital random microstructures with polydisperse pore size distributions corresponding to uniform frequency curves or histograms; isolated (A–D) or overlapping (E–H) pores; ϕ = porosity.
Figure 7. Examples of digital random microstructures with identical isolated pores with a diameter of 15 μm (monodisperse pore size distributions) and a different degree of repulsive interaction (excluded volume effects), i.e. a different minimum pore distance: 1 μm (A, B), 2 μm (C, D), 5 μm (E, F), 10 μm (G, H); ϕ = porosity.

Chapter 8

Figure 1. Temperature program used for pyrolysis in this study.
Figure 2. Apparatus of loading procedure.
Figure 3. Typical SEM image of (a) precursor material, (b) after pyrolysis. Cross sectional view of strut (pillar) is also shown in (c).
Figure 4. (a) Definition of minimum thickness of pillar (b) Distribution of minimum thickness in precursor material (c) Distribution of minimum thickness in TNPC.
Figure 5. Pore size distribution before and after pyrolysis.
Figure 6. (a) A typical example of slice image obtained by X-ray CT (b) Greyscale value distribution, (c) Binarized image (d) image processing procedure.
Figure 7. 3D model of TNPC after reconstruction using binarized images after masking.
Figure. 7(a) A typical stress-strain curve during the test. (b) Macroscopic fracture appearance at the maximum stress.
Figure. 8 Relationship between porosity and compressive strength of various carbon

Chapter 9

Figure 1. Structure of the air turbine with fluid-dynamic bearing system.
Figure 2. Cross-sectional view of the air turbine with fluid-dynamic bearing system.
Figure 3. Design of the multilayer ceramic magnetic circuit for 4-pole magnet and the fluid-dynamic type.
Figure 4. Structure of the air turbine with ball bearing system.
Figure 5. Cross-sectional view of the air turbine with ball bearing system.
Figure 6. Design of the multilayer ceramic magnetic circuit for 2 poles magnet
Figure 7. The assembled air turbine generator with fluid-dynamic bearing system.
Figure 8. The output waveform of the generator (Load resistance 1 Ω, Fluid-dynamic bearing system).
Figure 9. The assembled air turbine generator with ball bearing system.
Figure 10. The relations between load resistance and the output.
Figure 11. The output waveform of the generator (Load resistance 0.5 Ω, ball bearing system).
Figure 12. The output waveform of the generator (Load resistance 1000 Ω, ball bearing system).

Chapter 10

Table 1. X-ray fluorescence (XRF) analysis results (in wt.% of oxides) for kaolin and talc.
Figure 1. Particle size distributions of Czech kaolin (smaller size curves) and Australian talc (larger size curves); cumulative (solid) and frequency curves (dashed).
Figure 2. Thermal analysis of Czech kaolin (lower curves) and Australian talc (upper curves); thermogravimetric curves (dashed, left) and differential thermal analysis curves (solid, right).
Figure 3. Bar-shaped specimens after uniaxial pressing (40 MPa) and firing at 1280°C; from left to right: T100, K20T80, K40T60, K60T40, K80T20, K100.
Figure 4. Temperature dependence of Young’s moduli of as-fired magnesia-alumina-silicate ceramics of different composition (K100, K80T20, K60T40, K40T60, K20T80, T100) during heating and cooling (down).

Chapter 11

Figure 1. Microstructures of the materials hot pressed (30 MPa) from (a) α-AlB₁₂ powder (sample 2 in Table 2); (b) α-AlB₁₂ with 20% TiC (sample 9 in Table 2); and (c) α-AlB₁₂ with 12% TiC (sample 10 in Table 2).
Figure 2. (a, b) Microstructures (two the most representative areas under the same magnification) of the material synthesized from α-AlB₁₂+20 % TiC at 2 GPa, 1400°C for 0.17 h (sample 12 in Table 2, COMPO). Approximate composition of the present phases: darken gray matrix phase AlB₃₆O_0.8 - AlB₃₀Ti_0.006 - AlB₁₉Ti_0.002O2.27, phase looked bright - AlB₇₁₅O_1.17-3.6Ti_0.002-0.003 - AlB₈O₃C_2.7Ti_0.003. (c) Microstructure and distribution of the elements Al, B, C, O, Ti (EMP maps).
Figure 3. Representative microstructures of the sample hot pressed (30 MPa, 1950°C for 0.3 h) from α-AlB₁₂ powder with 17% C addition (sample 6 in Table 2) under different magnification. Approximate composition of the present phases: 1 – AlB_16.5 (dark gray matrix), 2 – AlB₁₆O_0.09-0.22 (light gray matrix), 3 – Al₂O_3.5B_0.6-4.8 (bright white inclusions), 4-BNC_0.3O_0.03-0.07 (the darkest inclusions).

Chapter 12

Fig 1. Effect of air pockets on over all breakdown. Lower emissivity (εr) and DBS of air can cause flashover in air pockets.
Fig 2. Dielectric strength of different ceramic bodies. Vitox material which has the highest density and chemical purity shows very high dielectric breakdown strength.
Fig 3. Microstructure (a) AL300, (b) AL500, (c) AL995, (d) Vitox, and (e) Generic alumina used in our study.
Fig 4. Mo/Mn coated alumina with Ni plating over Mo paint.

Chapter 15

Figure 1: XRD pattern (A) and FT-IR spectrum (B) of analyzed CFB ash.
Figure 2: SEM images of CFB ash activated with 5 (A), 6 (B), and 9 (C) M NaOH solution.
Figure 3: XRD patterns of alkali-activated CFB ash before (A) and after (B) sorption of Ni2+.
Figure 4: FT-IR spectra of alkali-activated CFB ash in whole (A) and smaller (B and C) wavenumber range.

Chapter 16

Figure 1: Dielectric constants (upper frames) and dielectric losses (lower frames) of ErMnO₃ single crystal. The left frames denote the temperature dependent properties for various frequencies (closed symbols) and the right frames the frequency dependent properties for various temperatures (open symbols).
Figure 2: Applied electric field (left axis) and resulting current flow (right axis) of a positive-upnegative-down measurement of ErMnO₃ at 120 K. The time span of each pulse corresponds to a frequency of 10 Hz.
Figure 3: Ferroelectric hysteresis loop measurement at 10 Hz of ErMnO₃ performed at 120 K with an excitation electric field up to 110 kV/cm.
Figure 4: Intersectional, multidisciplinary aspects of the material and product lifecycles. The four-level architecture represents basic research, technical development of a material for a prototypical application, application and the re-phase, displayed from bottom to the top. Each level includes the value chain of a material or product life cycle, their concomitant risks and suitable risk mitigation strategies. The arrows denote a predicted path for the development of ErMnO₃ based electronic functional units.

Chapter 19

Figure 1. Temperature dependence of the dielectric constant (a) and conductivity (b) of BMIM-Cl confined in MFU-4 (sample 1a) for various frequencies. The lines represent three frequencies of sample 1b, where the spectra have been recorded with reduced pressure. The inset (c) is the temperature dependence of the conductivity of sample 2 that has a lower loading fraction. The dashed lines with the arrows illustrate the intrinsic relaxation and the black dashed line indicates the dc conductivity.
Figure 2. Comparison of the temperature dependence of the conductivity of sample 1a and empty MFU-4 at selected frequencies. The dashed line indicates the dc-conductivity.
Figure 3. Relaxation times (closed symbols) and dc-conductivities (open symbols) in an Arrhenius representation of bulk BMIM CL and BMIM Cl confined in MFU-4. The data are revealed from the dielectric properties of sample 1a and sample 2. The properties of bulk BMIM-Cl were taken from Ref. 31. The dashed line represents a fit with the Vogel-FulcherTammann-equation. The dotted line serves as a guide to the eye for the confinement effect. The straight lines through the circles indicate the linearity of the conductivity in this representation.

Chapter 20

Figure 1. Thermal neutron detection capability vs. NaIL crystal thickness and lithium concentration for a 400 cm² crystal surface. The values are calculated from thermal neutron interaction cross-sections.
Figure 2. Averaged gamma-ray and neutron scintillation pulses for NaIL crystals with (a) 0.7% Li, (b) 2.2% Li and (c) 7.7% Li.
Figure 3. PSD-energy density contour plot for NaIL scintillation waveforms under irradiation from a moderated ²⁵²Cf source. Note the good separation between neutrons and gammas.
Figure 4. Plot of the detected neutron count rate vs the thermal neutron flux from the OSU-NRL reactor beam. The NaIL crystal, F23-35A, has dimensions ϕ2.5x2.5 cm and [⁶Li] = 1.37% (filled circles). F12-01C has dimensions ϕ5.1x5.1 cm and [⁶Li] = 0.23% (open circles).
Figure 5. (a) Scintillation light yield and (b) energy resolution (at 662 keV) of NaIL with different Li concentrations in crystal
Figure 6. a) photo of a large (~2100 cm³) crystal cut from a 120,000 cm³ NaIL ingot. b) the same crystal packaged in a hermetic housing for testing.
Figure 7. PSD and energy density contour plot for a large NaIL crystal (~5x10x40 cm³) irradiated with a moderated ²⁵²Cf source.

Chapter 21

Figure 1: XRD patterns of 80 nm h-LuFeO₃ thin films, deposited on (bottom) (0001) Al₂O₃ and (top) (111) YSZ at 800 °C and annealed at 850 °C. Only (00l) planes are observed, indicating the single crystalline quality of the thin films.
Figure 2: (a) ZFC and FC magnetic moment of a 80 nm h-LuFeO₃/Al₂O₃ thin film as a function of temperature for the out-of-plane (H || c-axis), showing a magnetic transition temperature T_N ~140 K. (b) M-H hysteresis loops measured at 4 K and 50 K for the h-LuFeO₃/Al₂O₃ thin film. The observation of smaller M-H loops is consistent with a canted antiferromagnetic state below T_N.
Figure 3: XRD patterns of (a) h-LuFeO₃/Al₂O₃ thin films and (b) h-LuFeO₃/YSZ thin films. Thin films were annealed at temperatures between 850–1050 °C, as labeled on the right side, before each x-ray scan. The xrd pattern for h-LuFeO₃/Al₂O₃ thin films changes at 950 °C with new peaks appearing in the 2θ= 30-40° range, indicating a structural phase change. In contrast, the xrd pattern for h-LuFeO₃/YSZ thin films remains unchanged after annealing in the same temperature range.
Figure 4: AFM Images of the h-LuFeO₃/Al₂O₃ thin film annealed at (left) 850 °C and (right) 1050 °C. The surface structures significantly increased after annealing the sample at 1050 °C.
Figure 5: (a) Room temperature absorption coefficient as a function of photon energy for the h-LuFeO₃/Al₂O₃ thin film, annealed at 900 °C and 1050 °C, respectively. The arrows indicate the electronic transitions for the 900 °C annealed thin film. (b) The direct energy band gap as a function of temperature, showing a broad peak around 150 K. (c) The upper energy band edge as a function of temperature for the 900 °C annealed h-LuFeO₃/Al₂O₃ thin film. The band edge changes the slope around the magnetic transition temperature 140 K. The inset shows an example of the energy band edge fitting with the direct energy band gap model.

Chapter 24

Figure 2. Optical microscope images of CuV₂O₆ on a mesoporous SiO₂ pellet (a, b) and on a quartz plate (c, d) in air. Left images are taken at room temperature and right images are after heating at 725°C.
Figure 3. Optical microscope images of CuV₂O₆ on a quartz plate in after heating at 725°C for 200 min.
Figure 4. (a) SEM and (b) BSE images after melting of CuV₂O₆ on a 3D-mesoporous SiO₂ pellet at 725°C. SEM and EDX spectra (c) and (d) were taken from areas shown in (a). Pt signals in EDX spectra are due to a conducting coating.
Figure 5. Raman spectra of residual solid after melting of CuV₂O₆ on a 3D-mesoporous SiO₂ pellet at 725°C (see Figures 2 and 4).
Figure 6. in situ SEM images of molten vanadate penetrating into mesoporous SiO₂ at >650°C. White arrows show the front line of the molten vanadate.
Figure 7. Schematic illustration of structural evolution from mesoporous to macroporous CuV₂O₆/SiO₂ via melting of CuV₂O₆, penetration of the melt into mesopores and dissolution-reprecipitation of SiO₂.

Chapter 25

Figure 1.a) The SPES production target, including a tantalum tube (heater) heated by Joule effect, a graphite box containing the seven target discs, a graphite window to avoid nuclei loss from the target towards the proton beam channel and three graphite dumps to stop the primary proton beam after its interaction with the target discs; b) Picture of the graphite box containing the discs.
Figure 2. Thermal characterization of UC_x: a) thermal conductivity; b) emissivity. The different datasets in b) are relative to materials with different composition and microstructural properties, produced in different labs in the framework of a European collaboration⁹.
Figure 3. Yield of Cd and Sn isotopes from different SPES UC_x targets: standard UC_x and low density UC_x (using MWCNTs).
Figure 4. a) seven La₂O₃ + C discs before the thermal treatment, contained in a graphite box; b) lanthanum carbide discs after the thermal treatment; c) main components of the furnace: the box containing the discs is inserted inside the tantalum heater, which is heated by Joule effect and surrounded by tantalum screens.
Figure 5. SEM images showing the microstructure of highly permeable lanthanum carbides obtained with different sacrificial fillers: a) PMMA microbeads; b) nylon fibers.

Chapter 26

Figure 1. The variation in spatial and temporal domains of different modelling approaches are illustrated¹.
Figure 2. Example temperature distribution calculated using the FAST code²¹ with finite-element mesh and labels overlaid.
Figure 3. A) The U-O phase diagram is illustrated on the left with experimentally measured phase transitions superimposed²². B) The U-Mo phase diagram is shown on the right with pertinent fuel compositions highlighted²⁶.
Figure 4. Snapshots of the time evolution of the intragranular bubble migrating and merging with the grain boundary, colored according to pressure. The simulation is azimuthally symmetric about the bottom boundary.
Figure 5. Interconnected intergranular porosity which accomodates fission gas within the solid fuel matrix. Left: example Scanning Electron Microscope images of advanced stages of grain boundary porosity formation^30,31. Right: The newly developed shell porosity model which qualitatively captures porosity morphology²⁹.

Chapter 27

Figure 1. Photocatalytic activity and weight loss of powders prepared from various precursors.
Figure 2. Weight loss through dehydration and condensation to crystallization.
Figure 3. XRD profiles of the TiO₂ powders prepared from various precursors: a) TIO-4, b) P25, c) W1.4, d) TH-ortho, e) TH-meta. Figure 4. FESEM images of TiO₂ powders prepared from various precursors: a) TIO-4, b) P25, c) W1.4, d) TH-ortho, e) TH-meta.
Figure 4. FESEM images of TiO₂ powders prepared from various precursors: a) TIO-4, b) P25, c) W1.4, d) TH-ortho, e) TH-meta.
Figure 5. Photos of TiO₂ coated concrete blocks before and after MB decomposition test, a) Comp10, b) Comp15, c) Comp20, left column: P25 and right column: W1.4.

Chapter 28

Figure 1. XRD patterns of the (Ba_1-xCa_x)TiO₃ powders at room temperature.
Figure 2. Lattice volume change with Ca concentration (x) in (Ba_1-xCa_x)TiO₃ powders.
Figure 3. SEM micrographs of the ceramic grains and WDX analyzed distribution of rare-earth elements in a (Ba_0.88Ca_0.12)TiO₃ dielectric.
Figure 4. Temperature-capacitance characteristics of rare-earth element doped (Ba_0.88Ca_0.12)TiO₃.
Figure 5. (a) Bright-field TEM image of (Ba,Ca)TiO₃ grains, indicating EDX measurement points (Y doped dielectrics) and (b) the variation in Y and Dy concentration as a function of the distance from the grain boundary.
Figure 6. The variation in the capacitance change at 150°C as a function of Ca concentration.
Figure 7. The mean time to failure as a function of the Ca concentration, according to a highly accelerated life test.
Figure 8. SEM micrographs of Gd doped and Y doped (Ba,Ca)TiO₃ dielectrics.
Figure 9. Distribution of Ca in the Y doped (Ba_1-x,Ca_x)TiO₃ dielectrics.
Figure 10. The relationship between Ca concentration and the activation energy, calculated using the MTTF in the HALT conditions for a Y doped dielectric.
Figure 11. The variation in the interaction energy between alkaline-earth elements and Vo in BaTiO₃, as a function of the ionic radius.
Figure 12. Schematic diagrams of the atomic structure around Ca and Vo in BaTiO3.
Figure 13. Relationship between capacitance changes at 150°C and the MTTF during HALT.
Figure 14. (a) Temperature-capacitance characteristics and (b) HALT results of MLCC with (Ba,Ca)TiO₃ based ceramics at 150°C.
Figure 15. MLCC appearance before and after high temperature load test at 200°C.
Figure 16. The structure of the developed adhesive compatible MLCC for usage at 200°C.
Figure 17. MLCC appearance after high temperature load test at 200°C

Chapter 29

Figure 1 Design of the multi-layer glass capacitor (Not to scale).
Figure 2 Etch rates across the useable portion of a 101 x 101 mm glass.
Figure 3 AFM scans showing the surface roughness for the unetched and etched samples. The RMS roughnesses are 1.64 nm and 4.12 nm, respectively.
Figure 4 Capacitance and loss for the 10 layer MLGC. The 5.5 nF capacitance indicates each layer is contributing 550 pF.
Figure 5 Unipolar hysteresis loop at 100 Hz. The capacitor exhibited minimal loss and a recoverable energy of 3.2 mJ.

Chapter 30

Figure 1. Depiction of CPSNP with active agents encapsulated and surface modification for targeted treatment.³¹
Figure 2. Synthesis flowchart for forming phase pure hydroxyapatite via a chemical precipitation reaction between calcium hydroxide and phosphoric acid.
Figure 3 (A) FDM 3D printer retrofitted for DIW of HA-hydrogel. (B) CAD model for spatial resolution testing. (C) Print path in Simplify3D for pore size analysis.
Figure 4 (A) 24 factorial design for spatial resolution analysis of FDM of PLA. (B) 23 factorial design for pore accuracy analysis of FDM of PLA.
Figure 5 2^4-1 factorial design for pore accuracy analysis of a DIW system of a HA-hydrogel.
Figure 6 (A) XRD analysis of synthesized and as received HA. (B) General data including lattice parameters from XRD Rietveld refinement, pH, and zeta potential (mean ± 95% CI, n=5). (C) FESEM of agglomerated HA primary particles. (D) FE-SEM of spray dried, as received HA.
Figure 7 (A) Photomicrograph of 24 factorial design for FDM of PLA. (B) Magnified photomicrograph of spatial resolution sample. (C) Optical profilometry image of spatial resolution sample.
Figure 8 (A) Photomicrograph of 2³ factorial design for FDM of PLA with center points for infill percentage. (B) Magnified photomicrograph of polymeric pores. (C) Optical profilometry image for determination of average pore size.
Figure 9 (A) Photomicrograph of 2^4-1 factorial design for pore size analysis of DIW HA-hydrogel. (B) Magnified photomicrograph of HA-hydrogel pores. (C) Optical profilometry image for determination of average pore size.

Preface

The Pacific Rim Conference on Ceramic and Glass Technology is a bi-annual conference held in collaboration with the ceramic societies of the Pacific Rim countries—The American Ceramic Society, The Chinese Ceramic Society, The Korean Ceramic Society, and the Australian Ceramic Society. The 1st PACRIM conference was hosted by The American Ceramic Society (ACerS) at Maui, Hawaii, in 1993. Over the years, PACRIM conferences have earned a distinct reputation as a premier forum for presentations and discussions on the state-ofthe-art and emerging topics in ceramics and glass technologies.

The 12th Pacific Rim Conference on Ceramic and Glass Technology (PACRIM 12) was held at the Hilton Waikoloa Village, Waikoloa, Hawaii, May 21-26, 2017. PACRIM 12 had 34 Symposia and drew a record number of attendees—nearly 1,200—to give 1,400 presentations and 250 posters. Scientist, engineers, and students from 44 countries attended the conference, attesting to the truly international nature of the field of materials science, and ceramic and glass science in particular.

This Ceramic Transactions volume contains 32 peer reviewed papers from the following symposia held during PACRIM 12:

Symposium 2: Virtual Materials Design and Ceramic Genome
Symposium 3: Novel, Green, and Strategic Processing and Manufacturing Technologies
Symposium 4: Polymer Derived Ceramics (PDCS) and Composites
Symposium 6: Synthesis and Processing of Materials using Electric Currents and Pressures
Symposium 7: Porous Ceramics
Symposium 10: Multifunctional Nanomaterials and Their Heterostructures for Energy and Sensing Devices
Symposium 11: Engineering Ceramics: Processing and Characterizations
Symposium 12: Design, Development and Applications of Ceramic Matrix Composites
Symposium 13: Advanced Structural Ceramics for Extreme Environments
Symposium 16: Geopolymers: Low-Energy and Environmental-Friendly Ceramics
Symposium 17: Advanced Functional Ceramics and Critical Materials Perspective
Symposium 20: Crystalline Materials for Electrical, Optical and Medical Applications
Symposium 22: Direct Thermal to Electrical Energy Conversion Materials and Applications
Symposium 23: Materials for Solar Thermal Energy Conversion and Storage
Symposium 25: Ceramics for Next Generation Nuclear Energy
Symposium 27: Ceramics for Enabling Environmental Protection: Clean Air and Water
Symposium 29: Advances in Polar, Magnetic and Semiconductor Materials: Extending Temperature Limits
Symposium 32: Nanostructured Bioceramics and Ceramics for Biomedical Applications
Third International Richard M. Fulrath Symposium on Discontinuous Progress for Ceramic Innovations
Young Investigator Forum: Design and Application of Next Generation Multifunctional Materials

The editors wish to extend their gratitude and appreciation to all the symposium co-organizers for their help and support, to all the authors for their cooperation and contributions, to all the participants and session chairs for their time and efforts, and to all the reviewers for their valuable comments and suggestions. We hope that these proceedings will serve as a useful resource for materials scientists and engineers.

DILEEP SINGH
Conference Chair
PACRIM 12

Proceedings of the
12th Pacific Rim
Conference on Ceramic
and Glass Technology

Ceramic Transactions, Volume 264

A Collection of Papers Presented at the 12th Pacific
Rim Conference on Ceramic and Glass Technology
May 21–26, 2017, Waikoloa, Hawaii

Preface

Multiscale Modeling and Simulation