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ISBN: 978-1-119-21169-3
ISSN: 0196-6219

CONTENTS

Preface

Introduction

Ceramics and Composites for Sustainable Nuclear and Fusion Energy

HOOP TENSILE STRENGTH OF CMC TUBES FOR LWRS APPLCATIONS USING INTERNAL PRESSURIZATION VIA ELASTOMERIC INSERT: NEW ASTM TEST METHOD
1. ABSTRACT
2. INTRODUCTION
3. ASTM STANDARD TEST METHOD
4. SCOPE AND APPLICATION
5. EXPERIMENTAL FACTORS
6. TEST SPECIMEN GEOMETRIES
7. TEST EQUIPMENT AND PROCEDURES
8. CALCULATION, REPORTING, PRECISION AND BIAS
9. CURRENT STATUS AND FUTURE WORK
10. CONCLUSIONS
11. ACKNOWLEDGEMENT
12. REFERENCES
PROPERTIES OF Al₂O₃ – CaO GLASS JOINTS OF SILICON CARBIDE TUBES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL PROCEDURE
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. REFERENCES
CORROSION-RESISTANT TERNARY CARBIDES FOR USE IN HEAVY LIQUID METAL COOLANTS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSIONS
6. ACKNOWLEDGMENTS
7. REFERENCES
DEVELOPMENT OF ACCIDENT TOLERANT SIC/SIC COMPOSITE FOR NUCLEAR REACTOR CHANNEL BOX
1. ABSTRACT
2. INTRODUCTION
3. SELECTION OF ACCIDENT TOLERANT CORE MATERIAL
4. SELECTION OF SIC MATRIX FABRICATION PROCESSES FOR ACCIDENT TOLERANT CORE MATERIAL
5. MATERIAL DESIGN OF CHANNEL BOX
6. SUMMARY
7. ACKNOWLEDGEMENT
8. REFERENCES
THERMAL DIFFUSIVITY MEASUREMENT OF CURVED SAMPLES USING THE FLASH METHOD
1. ABSTRACT
2. 1. INTRODUCTION
3. 2. THEORETICAL MODEL AND CALCULATION
4. 3. EXPERIMENTAL AND GEOMETRICAL FACTOR DETERMINATION
5. 4. APPLICATION TO COMPOSITES
6. 5. CONCLUSIONS
7. REFERENCES

Ceramics for Energy Generation, Conversion, and Rechargeable Energy Storage

GLASS CERAMIC SEPARATORS FOR ROOM TEMPERATURE OPERATING SODIUM BATTERIES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. REFERENCES
AVENUE TOWARDS THE DEVELOPMENT OF NEW NANOSTRUCTURED COMPOSITE CATHODE MATERIALS FOR LITHIUM-ION BATTERIES
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. ACKNOWLEDGEMENT
7. REFERENCES
COMPARATIVE STUDY OF POLYSULFIDE ENCAPSULATION IN THE DIFFERENT CARBONS PERFORMED BY ANALYTICAL TOOLS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL
4. RESULTS AND DISCUSSION
5. CONCLUSION
6. ACKNOWLEDGEMENTS
7. REFERENCES
PERFORMANCE STUDY OF LI-ION BATTERY ELECTRODES DRIED USING INLINE MICROWAVE HYBRID SYSTEM
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL PROCEDURE
4. RESULTS & DISCUSSION
5. SUMMARY
6. ACKNOWLEDGEMENTS
7. REFERENCES

Ceramic Materials and Processing for Photonics and Energy

COPPER CLAD ULTRA-THIN FLEXIBLE CERAMIC SUBSTRATE FOR HIGH POWER ELECTRONICS
1. ABSTRACT
2. INTRODUCTION
3. THIN E STRATE^® OVERVIEW
4. COPPER-CLADDING
5. COPPER-CLAD DESIGN SPECIFICATION WITH THIN E STRATE®
6. CUSTOMER EVALUATION AND TESTING
7. CUSTOMER (C1) ELECTRICAL EVALUATION
8. FUTURE PLANS
9. ACKNOWLEDGEMENTS
10. REFERENCES
ROLL-TO-ROLL ULTRATHIN FLEXIBLE CERAMIC FOR COST EFFECTIVE COATING
1. ABSTRACT
2. INTRODUCTION
3. WHY ROLL-TO-ROLL PROCESSING?
4. ADDRESSING THE CHALLENGE
5. SUMMARY
6. ACKNOWLEDGEMENTS
7. REFERENCES
NANOMATERIALS FOR ENERGY CONVERSION – THE SYNTHESIS OF HIGHLY CRYSTALLINE YTTERBIUM(III) FLUORIDE NANOPARTICLES FROM IONIC LIQUIDS
1. ABSTRACT
2. INTRODUCTION
3. EXPERIMENTAL DETAILS
4. CHARACTERIZATION
5. RESULTS AND DISCUSSION
6. CONCLUSIONS
7. ACKNOWLEDGEMENTS
8. References

Author Index

EULA

List of Illustrations

Chapter 1

Figure 1 SiC/SiC CMC cladding for LWR fuel rods (from Ref 1)
Figure 2 Range of “interferences” in test CMC materials
Figure 3 Illustration of test setup for insert testing (Ref. 10)
Figure 4 Calculation of hoop stress for elastomeric insert

Chapter 2

Figure 1. Braze SiC specimens: (A) tube and lid; (B) disks.
Figure 2 Cross section of the joint imaged using a confocal laser scanning microscope.
Figure 3. Confocal laser scanning microscope images of the morphology of the fractured joint after four point bending test: (A) right side; (B) left side.
Figure 4. Dependence of fracture load to joining temperature and time: (A) Fracture Load vs. temperature; (B) Fracture Load vs. time.
Figure 5. Confocal laser scanning microscope image of the cross section of the joint: (A) before autoclave test; (B) after autoclave test carried out at 500 °C, at a pressure of 25 MPa and at flow rate of a 1 m/s with oxygen content of 25 ppm for seven days.
Figure 6. Secondary electron and backscattered electron images of the cross section of the joint after autoclave test carried out at 500 °C, at a pressure of 25 MPa and at flow rate of 1 m/s with oxygen content of 25 ppm for seven days; a) secondary electron (SEM) image; b) backscattered electron (BSE) image.

Chapter 3

Figure 1. (A) Schematic representation of the CORELLA facility, which comprises two tanks: the HLM conditioning tank (right) and the testing tank (left). The test specimens are fixed on a holding plate that is attached to the rotating axis, the speed of which is measured and controlled during testing. Temperature and concentration of dissolved oxygen in the HLM are monitored by means of a thermocouple and an electrochemical oxygen sensor, respectively. The HLM oxygen concentration is controlled by bringing the HLM in equilibrium with the appropriate (oxidizing or reducing) conditioning gas phase. (B) Picture of the CORELLA facility.
Figure 2. Light optical microscopy pictures of materials tested during the refurbished CORELLA performance qualification test (i.e. liquid Pb, 100 h, 480°C, [O] < 10^-9 mass%, v ≈ 10 m/s). (A) MAXTHAL 312®: specimen side facing the Pb flow. The erosion assessment was challenging, due to the non-perfectly flat surface of the pristine specimen. Erosion damages - if any - were limited. (B) T91 f/m steel surface-modified with the GESA treatment: specimen side facing the Pb flow. Erosion damages were only observed on the small specimen facets (arrows) that have not been subjected to the surface modification treatment.
Figure 3. XRD patterns of the ceramics produced by the interrupted Ti₂SnC sintering cycles at 500, 700, 950 and 1200°C. α: Ti₂SnC, β: Ti₅Sn₃, γ: Sn, δ: TiC, ε: C, ζ: Ti₂Sn₃, η: Ti₆Sn₅, θ: Ti.
Figure 4. Temperature and shrinkage evolution as a function of time for the Ti2SnC sintering cycle at 1400°C. Regions (1)-(4) can be correlated to the reaction sequence during sintering.
Figure 5. XRD patterns of the Ti₂SnC ceramics sintered at a final sintering temperature in the 1200-1400°C range under a pressure of 50 MPa. α: Ti₂SnC, β: Ti₅Sn₃, γ: Sn, δ: TiC.
Figure 6. Backscattered electron (BSE) detector images of cross-sectioned Ti₂SnC ceramics sintered at (A) 1200°C, (B) 1300°C, (C) 1325°C and (D) 1400°C. The brightest areas are Sn-rich.
Figure 7. BSE detector images of polished cross-sections of (A) MAXTHAL 211^®, (B) MAXTHAL 312^® and (C) Nb₄AlC₃. Secondary electron detector images of the fracture surface of (D) MAXTHAL 211^®, (E) MAXTHAL 312^® and (F) Nb₄AlC₃.
Figure 8. Comparison of the flexural strength (A) and fracture toughness (B) of MAXTHAL 211^®, MAXTHAL 312^® and Nb₄AlC₃. The stars indicate the average grain size of the different MAX phase materials. The error bars show the standard deviation of all properties.
Figure 9. The normalized Young’s modulus (E/Ert) as function of temperature measured by IET. The vertical lines indicate the temperature where E/Ert = 0.75. Since the E/Ert of Nb₄AlC₃ has not been reduced to 0.75 at 1400°C, the superior thermal stability of this MAX phase is obvious.
Figure 10. BSE detector images of polished cross-sections of the non-exposed MAX materials (A) MAXTHAL 211®, (C) MAXTHAL 312® and (E) Nb₄AlC₃. BSE images of the same MAX material cross-sections after exposure for 3501 h at 500°C to poorly-oxygenated ([O] < 2.2×10^-10mass%) static LBE (B) MAXTHAL 211®, (D) MAXTHAL 312® and (F) Nb₄AlC₃.
Figure 11: Surface profilometry on test specimens before and after the 1^st erosion test. (A) Pristine and (B) exposed MAXTHAL 211^® specimen, with LBE residues, at the location of enhanced erosion damage. (C) Pristine and (D) exposed MAXTHAL 312^® specimen, with LBE residues, showing no signs of erosion damage.

Chapter 4

Figure 1. Cross-section view of channel box using this material design
Figure 2. Consideration of stress-strain curve for hybrid structure¹⁴⁾

Chapter 5

Fig. 1 Cross-section of a flat plate.
Fig. 2 Calculated rear surface temperature rise of a lead flat plate, 1.25mm thick.
Fig. 3 Cross section of cylindrical plate.
Fig. 4 Calculated temperature change on the center of the rear surface for a curved lead plate with an outer radius of 5cm.
Fig.5 Calculated temperature profile on rear surface for a curved lead plate when the center temperature reaches the maximum and half of the maximum.
Fig. 6 Calculated rear surface temperature change, taken at sample center and average of area viewed by detector aperture.
Fig. 7 Calculated results for time to reach half of the maximum temperature on rear surface as a function of outer radius, r
Fig. 8 Scheme of the experimental setup
Fig. 9 Experimental and calculated results for time to reach half of the maximum temperature on rear surface with the function of outer radius, r.
Fig. 10 Experimental data for the geometrical factor for lead samples at room temperature and a fitted curve (Eq. 8).
Fig. 11 Experimental data for the geometrical factor of stainless steel, along with the fitted curve for lead samples (Eq. 8).
Fig.12 (a) Representative void distribution for sample with higher void volume, (b) representative void distribution for overcoated sample with lower void volume.
Fig. 13 Effect of void volume fraction on thermal diffusivity.
Fig. 14 (a) Representative void distributions for a sample containing larger voids, (b) sample containing intermediate sized voids, and (c) sample containing smaller voids.
Fig. 15 Effect of voids size on thermal diffusivity.
Fig. 16 Representative cross-sections for combined monolith-composite tube structures having (a) lower monolith volume fraction, and (b) higher monolith volume fraction.
Fig. 17 Effect of monolith volume fraction on thermal diffusivity.

Chapter 6

Figure 1 Shrinkage behavior obtained using hot stage microscopy and images of quenched glass samples
Figure 2 Thermal analysis and linear shrinkage of ball milled powders
Figure 3 Density of ball and attrition milled powder of material A
Figure 4 Impedance Vs. Phase Shift (Left) and Conductivity of Different Sintering Temperatures
Figure 5 x-ray patterns for ball milled investigated materials >1100°C
Figure 6 Structure of unit cells of conductive phases
Figure 7 FESEM image of sintered powder compacts, left: ball milled powder ; right: attrition milled powder
Figure 8 Cross section of a sintered tape of attrition milled powder
Figure 9 translucent separators produced by tape casting; self-supporting sintering

Chapter 7

Figure 1. XRD patterns of the initial LiMn₂O₄ (1) and LiCoO₂ (6), and mechanocomposites (1-x)LiCoO₂/xLiMn₂O₄: x=0.7 (2); 0.6 (3); 0.5 (4); 0.4 (5).
Figure 2. Rietveld refined XRD patterns of the as-prepared mechanocomposite 0.5LiCoO₂/0.5LiMn₂O₄(1) and the product formed after the 12^th cycle (2).
Figure 3. SEM images of the initial LiCoO₂ (a), LiMn₂O₄ (b) and mechanocomposite 0.5LiCoO₂/0.5LiMn₂O₄ (c).
Figure 4. Typical charge-discharge profiles (a) and discharge capacity vs. cycle number plot (b) for mechanocomposites (1-x)LiCoO₂/xLiMn₂O₄: x = 0.7 (1); 0.6 (2); 0.5 (3); 0.4 (4).
Figure 5. dQ/dV vs. voltage plots for the first eleven cycles of the 0.5LiCoO₂/0.5LiMn₂O₄ mechanocomposite.
Figure 6. Multiphase Rietveld refined XRD pattern of the 0.5LiFePO₄/0.5Li₃V₂(PO₄)₃ mechanocomposite.
Figure 7. ⁵⁷Fe Mössbauer spectrum of the 0.5 LiFePO₄/0.5Li₃V₂(PO₄)₃ mechanocomposite.
Figure 8. Charge-discharge profiles (a) and specific capacity vs. cycle rate plot (b) for the 0.5LiFePO₄/0.5Li₃V₂(PO₄)₃ mechanocomposite.
Figure 9. A set of XRD patterns obtained during the charge of the 0.5LiFePO₄/ 0.5Li₃V₂(PO₄)₃ composite by in situ synchrotron diffraction (λ=0.20727 Å).
Figure 10. In situ XRD patterns of the products formed in the VPO₄+ LiF activated mixture under heating and cooling in a temperature-controlled chamber of a Bruker diffractometer.
Figure 11. Rietveld refined XRD patterns of phase-pure LiVPO₄F (a) and the LiVPO₄F/Li₃V₂(PO₄)₃ composite (b).
Figure 12. Charge-discharge profiles of phase-pure LiVPO₄F and the LiVPO₄F/Li₃V₂(PO₄)₃composite (a) and the dQ/dV vs. voltage plots (b) in the 3.0-4.5 V range at C/10 rate.
Figure 13. Charge-discharge capacity vs. cycling rate (C/10 – 10 C) plot for phase-pure LiVPO₄F and the LiVPO₄F/Li₃V₂(PO₄)₃ composite in the 3.0-4.5 V range.
Figure 14. SEM images of pristine (a) and Al₂O₃-coated LiCoO₂ prepared by solution (b) and by MA (c) methods.
Figure 15. ²⁷Al NMR spectra of the Al₂O₃-coated LiCoO₂ samples annealed at 400 (1) and 800°C (2).
Figure 16. Specific discharge capacity of pristine and coated LiCoO₂ vs. cycle number in the 3–4.5 V range.
Figure 17. SEM images of pristine (a) and LiCoO₂-coated LiMn₂O₄ by solution (b) and by MA (c) methods.
Figure 18. Specific discharge capacity of pristine and coated LiMn₂O₄ vs. the cycle rate.

Chapter 8

Figure 1. Discharge capacity (left axis) and columbic efficiency (right axis) from the composites prepared by using carbon black with different surface areas.
Figure 2. Electrochemical discharge/charge curves of selected cycles from a) Vul carbon/S composite electrode, b) PRX carbon/S composite electrode and c) MAX carbon/S composite electrode.
Figure 3. UV-Vis spectra measured in operando mode during the 1^st cycle of the Li-S battery with MAX/S composite and 1 M LiTFSI in sulfolane electrolyte: a) all spectra measured during discharge, b) all spectra measured during charge, and c,d) corresponding first-order derivatives of the UV-Vis spectra (the color change in all figures from the start to the end is from red through green to blue).
Figure 4. UV-Vis spectra measured in operando mode during the 1^st cycle of the Li-S battery with PRX/S composite and 1 M LiTFSI in sulfolane electrolyte: a) all spectra measured during discharge, b) all spectra measured during charge, and c, d) corresponding first-order derivatives of the UV-Vis spectra (the color change in all figures from the start to the end is from red through green to blue).
Figure 5. UV-Vis spectra measured in operando mode during the 1^st cycle of the Li-S battery with Vul/S composite and 1 M LiTFSI in sulfolane electrolyte: a) all spectra measured during discharge, b) all spectra measured during charge and c, d) corresponding first-order derivatives of the UV-Vis spectra (the color change in all figures from the start to the end is from red through green to blue).
Figure 6. Recalculated concentrations of short-, mid-and long-chain polysulfides detected in the separators of the battery from three types of composites. The black line corresponds to the measurement with PRX composite, the red line corresponds to MAX composite measurement, and blue line corresponds to measurement with Vul composite with 1 M LiTFSI sulfolane electrolyte.
Figure 7. a,c,e) Electrochemical behavior during the first reduction of carbon/S composites with different surface areas and cumulative charges obtained by the integration of individual CV scans. b,d,f) Corresponding CV scans measured for each Δx= 0.1 change of composition in Li_xS.

Chapter 9

Figure 2: Concept of microwave hybrid heating
Figure 3: (a) BTU's inline MW system (b) Electrodes entering into the MW exposure zone
Figure 4: Coin cells prepared using microwave dried electrodes
Figure 5: Moisture content in microwave dried (a) NMC532-NMP (b) NMC532-Aqueous (c) A12-NMP and (d) A12-Aqueous samples
Figure 6: Cyclic performance study of NMC532-NMP samples (a) 1 (b) 3 (c) 5 and (d) their comparison with baseline electrode
Figure 7: Cyclic performance study of NMC532-aqueous samples (a) 1 (b) 3 and (c) their comparison with baseline electrode
Figure 8: Cyclic performance study of A12-NMP samples (a) 1 (b) 3 (c) 5 and (d) their comparison with baseline electrode
Figure 9: Cyclic performance study of A12-aqueous samples (a) 3 (5) and (c) their comparison with baseline electrode
Figure 10: Microstructure of NMC532-NMP and A12-NMP electrodes before and after 103 minutes microwave exposure time

Chapter 10

Figure 1 - 50 cm strip of Thin E-Strate®.
Figure 2 - Twisting of sintered 40μm thick Thin E-Strate®.
Figure 3 - 20 microns thick Thin E- Strate® in foreground, 40 microns thick in back.
Figure 4 - Thin E- Strate® readily passes heat through plane.
Figure 5 - LED circuit on 40 microns thick Thin E-Strate® substrate with etched copper laminate circuit. Inset photo shows etched copper circuit substrate.
Figure 6 - Panelized customer test circuits.
Figure 7 – Unsupported Thin E Strate^®damaged during high-pressure wash.
Figure 8 – C1 test evaluation circuits.
Figure 9 - C1 test circuit.
Figure 10 - Resistance measurement data set.
Figure 11 - TDR measurements.
Figure 12 - S11 test measurements.
Figure 13 - S21 test measurements.

Chapter 11

Figure 1 – Flexibility of ENrG’s Thin E-Strate^® 40 microns thick fired ceramic.
Figure 2 - Charring of a marshmallow from a blowtorch applied to the opposite side of the 40 microns thick Thin E-Strate®.
Figure 3 - Thin E-Strate® is the dense electrolyte in a cross-section of a SOFC.(Courtesy of Fraunhofer IKTS).
Figure 4 - Thin E-Strate® handled by rollers.
Figure 5 - 50 cm strip of Thin E- Strate®.

Chapter 12

Figure 1. Powder X-ray diffraction pattern of synthesized YbF₃. a) Database pattern simulated from ICSD 9844, b) YbF₃ synthesized with [C₄mim][BF₄] by in the furnace, c) with [P₄₄₄₁₄][BF₄] in the furnace, d) with [C₄mim][BF₄] in the microwave, e) with [P₄₄₄₁₄][BF₄] in the microwave.
Figure 2. TEM micrographs and YbF₃ particles synthesized from [C₄mim][BF₄] in the furnace.
Figure 3. YbF₃ particles synthesized from [C₄mim][BF₄] in the microwave.
Figure 4. YbF₃ particles synthesized from [P₄₄₄₁₄][BF₄] in the furnace.
Figure 5. YbF₃ particles synthesized from [P₄₄₄₁₄][BF₄] under microwave irradiation.

Preface

This proceedings issue contains contributions from three energy related symposia that were part of the 39th International Conference on Advanced Ceramics and Composites (ICACC), in Daytona Beach, Florida, January 25-30, 2015:

Advanced Ceramics and Composites for Sustainable Nuclear Energy and Fusion Energy
Advanced Materials and Technologies for Energy Generation, Conversion, and Rechargeable Energy Storage
Advanced Ceramic Materials and Processing for Photonics and Energy

The first two symposia were sponsored by The American Ceramic Society's (ACerS) Engineering Ceramics Division and the third by ACerS Nuclear & Environmental Technology Division.

The editors wish to thank the authors and presenters for their contributions, the symposium organizers for their time and labor, and all the manuscript reviewers for their valuable comments and suggestions. Acknowledgment is also due for financial support from the Engineering Ceramics Division, the Nuclear & Environmental Technology Division, and The American Ceramic Society. The editors wish to thank ACerS for assembling and publishing the proceedings.

JOSEF MATYÁŠ, Pacific Northwest National Laboratory, USA
YUTAI KATOH, Oak Ridge National Laboratory, USA
HUA-TAY LIN, Guangdong University of Technology, China
ALBERTO VOMIERO, Luleå University of Technology, Sweden

Introduction

This CESP issue consists of papers that were submitted and approved for the proceedings of the 39th International Conference on Advanced Ceramics and Composites (ICACC), held January 25–30, 2015 in Daytona Beach, Florida. ICACC is the most prominent international meeting in the area of advanced structural, functional, and nanoscopic ceramics, composites, and other emerging ceramic materials and technologies. This prestigious conference has been organized by the Engineering Ceramics Division (ECD) of The American Ceramic Society (ACerS) since 1977.

The 39th ICACC hosted more than 1,000 attendees from 40 countries and over 800 presentations. The topics ranged from ceramic nanomaterials to structural reliability of ceramic components which demonstrated the linkage between materials science developments at the atomic level and macro level structural applications. Papers addressed material, model, and component development and investigated the interrelations between the processing, properties, and microstructure of ceramic materials.

The 2015 conference was organized into the following 21 symposia and sessions:

Symposium 1	Mechanical Behavior and Performance of Ceramics and Composites
Symposium 2	Advanced Ceramic Coatings for Structural, Environmental, and Functional Applications
Symposium 3	12th International Symposium on Solid Oxide Fuel Cells (SOFC): Materials, Science, and Technology
Symposium 4	Armor Ceramics: Challenges and New Developments
Symposium 5	Next Generation Bioceramics and Biocomposites
Symposium 6	Advanced Materials and Technologies for Energy Generation and Rechargeable Energy Storage
Symposium 7	9th International Symposium on Nanostructured Materials and Nanocomposites
Symposium 8	9th International Symposium on Advanced Processing & Manufacturing Technologies for Structural & Multifunctional Materials and Systems (APMT), In Honor of Prof. Stuart Hampshire
Symposium 9	Porous Ceramics: Novel Developments and Applications
Symposium 10	Virtual Materials (Computational) Design and Ceramic Genome
Symposium 11	Advanced Materials and Innovative Processing ideas for the Industrial Root Technology
Symposium 12	Materials for Extreme Environments: Ultrahigh Temperature Ceramics (UHTCs) and Nanolaminated Ternary Carbides and Nitrides (MAX Phases)
Symposium 13	Advanced Ceramics and Composites for Sustainable Nuclear Energy and Fusion Energy
Focused Session 1	Geopolymers, Chemically Bonded Ceramics, Eco-friendly and Sustainable Materials
Focused Session 2	Advanced Ceramic Materials and Processing for Photonics and Energy
Focused Session 3	Materials Diagnostics and Structural Health Monitoring of Ceramic Components and Systems
Focused Session 4	Additive Manufacturing and 3D Printing Technologies
Focused Session 5	Single Crystalline Materials for Electrical, Optical and Medical Applications
Focused Session 6	Field Assisted Sintering and Related Phenomena at High Temperatures
Special Session	2nd European Union-USA Engineering Ceramics Summit
Special Session	4th Global Young Investigators Forum

The proceedings papers from this conference are published in the below seven issues of the 2015 CESP; Volume 36, Issues 2-8, as listed below.

Mechanical Properties and Performance of Engineering Ceramics and Composites X, CESP Volume 36, Issue 2 (includes papers from Symposium 1)
Advances in Solid Oxide Fuel Cells and Electronic Ceramics, CESP Volume 36, Issue 3 (includes papers from Symposium 3 and Focused Session 5)
Advances in Ceramic Armor XI, CESP Volume 36, Issue 4 (includes papers from Symposium 4)
Advances in Bioceramics and Porous Ceramics VIII, CESP Volume 36, Issue 5 (includes papers from Symposia 5 and 9)
Advanced Processing and Manufacturing Technologies for Nanostructured and Multifunctional Materials II, CESP Volume 36, Issue 6 (includes papers from Symposia 7 and 8 and Focused Sessions 4 and 6)
Ceramic Materials for Energy Applications V, CESP Volume 36, Issue 7 (includes papers from Symposia 6 and 13 and Focused Session 2)
Developments in Strategic Ceramic Materials, CESP Volume 36, Issue 8 (includes papers from Symposia 2, 10, 11, and 12; from Focused Sessions 1 and 3); the European-USA Engineering Ceramics Summit; and the 4th Annual Global Young Investigator Forum

The organization of the Daytona Beach meeting and the publication of these proceedings were possible thanks to the professional staff of ACerS and the tireless dedication of many ECD members. We would especially like to express our sincere thanks to the symposia organizers, session chairs, presenters and conference attendees, for their efforts and enthusiastic participation in the vibrant and cutting-edge conference.

ACerS and the ECD invite you to attend the Jubilee Celebration of the 40th International Conference on Advanced Ceramics and Composites (http://www.ceramics.org/daytona2016) January 24-29, 2016 in Daytona Beach, Florida.

To purchase additional CESP issues as well as other ceramic publications, visit the ACerS-Wiley Publications home page at www.wiley.com/go/ceramics.

JINGYANG WANG, Institute of Metal Research, Chinese Academy of Sciences, Shenyang, China

SOSHU KIRIHARA, Osaka University, Osaka, Japan

Volume Editors
July 2015

A Collection of Papers Presented at the 39th International Conference on Advanced Ceramics and Composites January 25-30, 2015 Daytona Beach, Florida

A Collection of Papers Presented at the
39th International Conference on
Advanced Ceramics and Composites
January 25-30, 2015
Daytona Beach, Florida