Published by John Wiley & Sons, Inc., Hoboken, New Jersey.
Published simultaneously in Canada.

No part of this publication may be reproduced, stored in a retrieval system, or transmitted in any form or by any means, electronic, mechanical, photocopying, recording, scanning, or otherwise, except as permitted under Section 107 or 108 of the 1976 United States Copyright Act, without either the prior written permission of the Publisher, or authorization through payment of the appropriate per-copy fee to the Copyright Clearance Center, Inc., 222 Rosewood Drive, Danvers, MA 01923, (978) 750-8400, fax (978) 750-4470, or on the web at www.copyright.com. Requests to the Publisher for permission should be addressed to the Permissions Department, John Wiley & Sons, Inc., 111 River Street, Hoboken, NJ 07030, (201) 748-6011, fax (201) 748-6008, or online at http://www.wiley.com/go/permission.

Limit of Liability/Disclaimer of Warranty: While the publisher and author have used their best efforts in preparing this book, they make no representations or warranties with respect to the accuracy or completeness of the contents of this book and specifically disclaim any implied warranties of merchantability or fitness for a particular purpose. No warranty may be created or extended by sales representatives or written sales materials. The advice and strategies contained herein may not be suitable for your situation. You should consult with a professional where appropriate. Neither the publisher nor author shall be liable for any loss of profit or any other commercial damages, including but not limited to special, incidental, consequential, or other damages.

For general information on our other products and services or for technical support, please contact our Customer Care Department within the United States at (800) 762-2974, outside the United States at (317) 572-3993 or fax (317) 572-4002.

Wiley also publishes its books in a variety of electronic formats. Some content that appears in print may not be available in electronic formats. For more information about Wiley products, visit our web site at www.wiley.com.

Library of Congress Cataloging-in-Publication Data is available.

ISBN: 978-1-119-23448-7
ISSN: 1042-1122

CONTENTS

Preface

High-Temperature Fuel Cells and Electrolysis

Effect of Additives on Self-Healing of Plasma Sprayed Ceramic Coatings
Development of Ceramic Functional Layers for Solid Oxide Cells
BICU(TI)VOX as a Low/Intermediate Temperature SOFC Electrolyte:honey Another Look
Symbolic Analysis of Multi-Stage Electrochemical Oxidation for Enhancement of Electric Efficiency of SOFCS
Low Temperature AC Electric Field-Assisted Sintering of Unitary Anode-Supported Soled Oxide Fuel Cell
SOFC System Development and Held Trials for Commercial Applications
Technology Readiness of SOFC Stacks - A Review
High-Temperature Direct Fuel Cell Material Experience
Development of Highly-Efficient Energy Storage System Using Soled Oxide Electrolysis Cell

Ceramic-Related Materials, Devices, and Processing for Heat-to-Electricity Direct Conversion

Thermoelectric Properties Higher Manganese Silicide Containing Small Amount of Mnsivsinano-Particles
Anomalous Temperature Gradient Innon-Maxwellian Gases
Thermophysical Property of Poly-Si Phonomc Crystals for Thermoelectrics
The Potential of Maximal ZT-Value for Thermoelectric Materials of Mil ISi 19 HMS Phase by Calculating Electronic Structure

Material Science and Technologies for Advanced Nuclear Fission and Fusion Energy

Development of Ga Doped Hollandites Ba_xCs_y(Ga_2x+yTi_8-2x-y)O₆ for Cs Immobilization
Atomistic Simulations of Ceramic Materials Relevant for Nuclear Waste Management:honey Cases of Monazlte and Pyrochlore
Development of Joining Method for Zircaloy and SiC/SiC Composite Tubes by Using Fiber Laser

Advanced Batteries and Supercapacitors for Energy Storage Applications

An Investigation on the Cycle Performance of LiFePO₄ Pouch Cells by a Combination of Synchrotron Based X-ray Diffraction and Absorption Spectroscopy
The Influence of the Synthesis Route on Electrochemical Properties of Spinel Type High-Voltage Cathode Material LiNi_0.5Mn_1.5O₄ for Lithium Ion Batteries

Materials for Solar Thermal Energy Conversion and Storage

High Temperature Solar Receiver with Ceramic Materials
Determination of Parameters for Improved Efficiency in Thermal Energy Storage Using Encapsulated Phase Change Materials
Tuning the Spectral Selectivity of Sic-Based Volumetric Solar Receivers With Ultra-High Temperature Ceramic Coatings
Thermo-Mechanical Analysis of a Silicon Carbide Honeycomb Component Applied as an Absorber for Concentrated Solar Radiation

High-Temperature Superconductors:honey Materials, Technologies, and Systems

Anomalous Proximity Effect and More Than one Majorana Fermion
Atomic-Scale Study of the Superconducting Proximity Effect in Manganite/Cuprate Thin-Film Heterostructures
Tunneling and Photoemission Spectra in Cuprate Superconductors:honey Evidence for Strong Multiple-Phonon Coupling and Polaronic Effects

Author Index

EULA

List of Tables

Effect of Additives on Self-Healing of Plasma Sprayed Ceramic Coatings

Table 1
Table 2

BICU(TI)VOX as a Low/Intermediate Temperature SOFC Electrolyte:honey Another Look

Table I

Symbolic Analysis of Multi-Stage Electrochemical Oxidation for Enhancement of Electric Efficiency of SOFCS

Table 1

SOFC System Development and Held Trials for Commercial Applications

Table 1
Table 2
Table 3
Table 4

Technology Readiness of SOFC Stacks - A Review

Table 1
Table 2
Table 3
Table 4
Table 5
Table 6
Table 7
Table 8

High-Temperature Direct Fuel Cell Material Experience

Table 1
Table 2
Table 3

Development of Highly-Efficient Energy Storage System Using Soled Oxide Electrolysis Cell

Table I
Table II
Table III

The Potential of Maximal ZT-Value for Thermoelectric Materials of Mil ISi 19 HMS Phase by Calculating Electronic Structure

Table I

Development of Ga Doped Hollandites Ba_xCs_y(Ga_2x+yTi_8-2x-y)O₆ for Cs Immobilization

Table 1
Table 2
Table 3

Atomistic Simulations of Ceramic Materials Relevant for Nuclear Waste Management:honey Cases of Monazlte and Pyrochlore

Table I
Table II

Development of Joining Method for Zircaloy and SiC/SiC Composite Tubes by Using Fiber Laser

Table 1

The Influence of the Synthesis Route on Electrochemical Properties of Spinel Type High-Voltage Cathode Material LiNi_0.5Mn_1.5O₄ for Lithium Ion Batteries

Table I.

High Temperature Solar Receiver with Ceramic Materials

Table 1

Determination of Parameters for Improved Efficiency in Thermal Energy Storage Using Encapsulated Phase Change Materials

Table I.
Table II.

Tuning the Spectral Selectivity of Sic-Based Volumetric Solar Receivers With Ultra-High Temperature Ceramic Coatings

Table 1:
Table 2:

Thermo-Mechanical Analysis of a Silicon Carbide Honeycomb Component Applied as an Absorber for Concentrated Solar Radiation

Table 1
Table 2

List of Illustrations

Effect of Additives on Self-Healing of Plasma Sprayed Ceramic Coatings

Figure 1: Schematic of the SOFC stack sealing based on active braze and insolating coating.
Figure 2: Comparison of TGA/DSC profiles of submicron and nano SiC powders (a) and SiC+Y₂O₃ mixtures with submicronic or nano sized SiC (b). Note here that the weight gain values are given with respect to the SiC weight, while the DSC values are as obtained.
Figure 3: TGA/DSC data of submicron SiC and additives, AI₂O₃, TiO₂, GDC and Ta₂O₅, which show little influence on SiC oxidation. Note here that the weight gain values are given with respect to the SiC weight, while the DSC values are as obtained.
Figure 4: TGA/DSC data of submicron SiC and additives, which show remarkable differences in weight and/or DSC from those of pure SiC. (a) CaO, BaO, La₂Q₃, (b) GeO₂.
Figure 5: TGA/DSC data of SiC and additives: Y₂O₃ and ZnO
Figure 6: XRD patterns (zeroed base line) of SiC powder (a) and SiC+Al₂Q₃ mixture (b) before and after TGA/DSC measurements.
Figure 7: XRD patterns of the mixtures before and after TGA/DSC (zeroed base line): (a) SiC+CaO, (b) SiC+GeO₂.
Figure 8: XRD patterns of the mixtures before and after TGA/DSC (zeroed base line): (a) SiC+Y₂O₃, (b) SiC+ZnO.
Figure 9: Raman spectra of nano SiC (a) and nano SiC+ZnO (b) heat treated at 1050°C in air for different times and after TGA measurement. The peaks appeared at 868, 903 and 942 cm-¹ are the Raman modes of Zn₂SiO₄.
Figure 10: SEM of (a) self-healing coating: Bright additive particles are distnbuted in dark spinel matrix, (b) a splat of additive material. Dark particles are SiC and bright zone is Y₂O₃.
Figure 11: (a) SEM micrographs of self-healing ceramic coating of in as-sprayed condition, and (b) of same zone and magnification after heat treatment at 1050°C for 1 hour in air.
Figure 12: (a and c) Micrographs of fractured self-healing ceramic coating in as-sprayed condition, and (b and d) same zone and magnification after heat treatment at 1050°C for 5 hours (b) and 10 hour (d) in air.
Figure 13: Electrical resistance values for MgAl₂O₄ and MgAl₂O₄+20wt% (SiC+Y₂O₃) coatings.

Development of Ceramic Functional Layers for Solid Oxide Cells

Figure 1. Principle of planar SOC design according to DLR spray concept
Figure 2. Cassette arrangement with plasma sprayed cells for stack assembly
Figure 3. SEM image of typical morphology of the metallic PM Fe-26Cr-(Mo,Ti,Mn,Y₂O₃) porous substrate from Plansee
Figure 4. Metallographic cross-section of an entirely plasma sprayed cell on metallic support
Figure 5. Schematic of the EVOLVE type cell
Figure 6. SEM of NiCrAl foam and NiCrAl-LST substrates: (a) top view of NiCrAl foam, (b) top view of MCrAl foam fired with impregnated LST ceramic, (c) top view of the anode functional layer LST-GDC, (d) top view of the YSZ layer after dip coating (non sintered)¹⁵
Figure 7. SEM of half cells with dip-coated YSZ layer and EB-PVD GDC layer: (a) overview cross section, (b) top view of GDC layer, (c) cross section at LST-GDC/YSZ/GDC interfaces, (d) elemental mapping at LST-GDC/YSZ/GDC interfaces¹⁵.

BICU(TI)VOX as a Low/Intermediate Temperature SOFC Electrolyte:honey Another Look

Figure 1. Tetragonal unit cell of the high temperature γ-phase of Bi₄V₂O₁₁ (BIVOX). (Structural data from F. Abraham et al.⁴)
Figure 2. Total conductivity for BIVOX and BBVIEVOX ceramics (after Fuierer, et al. ¹³)
Figure 3. Aerosol deposition (AD) of BICUTIVOX Cross-sectional view of a 4 μm thick film on an alumina substrate. Conductivity of an AD film before and after heat treatment, compared to a bulk ceramic and screen print film. (Reprinted from [31] with permission from Elsevier.)
Figure 4. Schematic of processing schemes used for BICU(TI)VOX ceramics.
Figure 5. BICUVOX powders produced via (A) conventional calcining and (3-stage) milling, and (B) molten salt synthesis (650°C/8 hrs.).
Figure 6. BICUVOX microstructures, a) OF b) MSS-OF c) HFd) HF-tgg. (inset matches the magnification of (a)-(c)) * Appearance of grain boundaries in (d) were enhanced for visibility using non-linear adjustments to contrast and brightness.
Figure 7. BICUITVOX microstructures, a) HF (low mag) b) HF (high mag) c) OF (high mag). (Reprinted from [37] with permission from Elsevier.)
Figure 8. Thermal coefficient of expansion for BICUVOX (left) and BICUTIVOX (right).
Figure 9. Hysteresis in conductivity for BICUVOX ceramics. The lower branch is heating, upper is cooling for each sample. Line aids the eye for the HFperp sample.
Figure 11. Thermal aging of BICUVOX held at 400°C (left) and held at 500°C (right)
Figure 12. pO₂ stability of BICUVOX held at 400°C (left) and held at 500°C (right).

Symbolic Analysis of Multi-Stage Electrochemical Oxidation for Enhancement of Electric Efficiency of SOFCS

Figure 1. Schematic illustrations of the examples of the multi-stage electrochemical oxidation design: (a) segmented-in-series type stack, (b) planar type stacks with a series connection of fuel supply.
Figure 2. Uf_D as a function of Uf_T (n is from 2 to 20).
Figure 3. Uf_DL as, afunction of n at Uf_T =85% with the gas leakage or oxide-ion leakage.

Low Temperature AC Electric Field-Assisted Sintering of Unitary Anode-Supported Soled Oxide Fuel Cell

Figure 1: Sketch of temperature, voltage and current profiles during experiments on flash sintering.
Figure 2: Simple setup for flash sintering experiments: sample holder, furnace and power supply. Electric circuit: Vac - power supply; V - digital voltmeter; Pt - platinum electrode.
Figure 3: Dilatometric curves of anode-supported planar SOFCs from RT to 1200°C without (left) and with (right) application of an electric field (310 V.cm^-1) for 5 min.
Figure 4: Dilatometric curves of anode-supported planar SOFC from RT to 1100°C (left) and to 1200°C with application of an electric field (310 V.cm^-1) for 5 min.
Figure 5: Typical voltage, current and power during the flash sintering experiment.
Figure 6: Left - scanning electron microscopy image of a cross section of a unitary planar SOFC after flash sintering at 1100°C. LSM: Lanthanum Strontium Manganite cathode; YSZ: 8 mol% yttria-stabilized zirconia solid electrolyte; YSZ+NiO: anode; right - EDS results on the anode and cathode sides.
Figure 7 (a and b): Top - Scanning electron microscopy images of the components of a unitary planar SOFC after flash sintering at 1100°C. YSZ-MO: anode; YSZ: 8 mol% yttria-stabilized zirconia solid electrolyte; LSM: Lanthanum Strontium Manganite cathode. Bottom - Results of EDS analysis.
Figure 8: Impedance diagrams of of a unitary planar SOFCs after flash sintering at 1100°C and after co-sintering at 1200°C (conventional). Input signal 200 mV; frequency range 5 Hz-13 MHz: temperature 590°C. Green and red - experimental data; black - deconvolved (bulk and grain boundary) data.
Figure 9: Scanning electron microscopy image of the anode region of a unitary planar SOFC after flash sintering at 1100°C with 310 V.cm^-1, 5 A. YSZ: fully dense 8 mol% yttria-stabilized zirconia: Ni: metallic nickel after reduction of nickel oxide.
Figure 10: SEMimages of the cross section of green (a) and flash sintered (b) SOFC tape. See text for details.

SOFC System Development and Held Trials for Commercial Applications

Figure 1. Project phases of the SOFC system development for commercial applications.
Figure 2. Exploded view of eneramic® SOFC stack (left) and CFY SOFC stack (right).
Figure 3. Generic SOFC system integration approach.
Figure 4. Schematic representation of the multi-level simulation supported SOFC system development concept.
Figure 5. Sectional view of the eneramic^® HotBox (left) and h2e^® HotBox (right).
Figure 6. Endurance operation of an eneramic® HotBox, fueled by lab-grade propane.
Figure 7. Power output and stack operating temperature during automated start/stop-cyclisation tests with sample HotBoxes of generation 1 to 4 (HB-4 test ongoing).
Figure 8. Field trials with eneramic® prototype systems, powering a LED traffic control panel (left) and a cathodic corrosion protection device at an underground pipeline (right).
Figure 9. Sample data of the eneramic® field trial, powering a LED traffic control panel via a standard lead-acid battery (12 Vdc, 160 Ah).
Figure 10. Sample pictures of the h2e® HotBox assembly; 1) ceramic base plates with integrated reformer and afterburner; 2) 50 cell CFY stack mounted on baseplates; 3) assembled HotBox with thermal insulation; 4) prototype HotBox mounted in laboratory test-rig for verification test.
Figure 11. Design verification test with the h2e® HotBox prototype, installed in a laboratory test-rig (1 .000 hours endurance operation, followed by automated start/stop-cyclisation test, fueled by lab-grade methane during all tests).
Figure 12. Sample views of h2e® Proof-of-Concept prototype systems during assembly.
Figure 13. h2e® Proof-of-Concept prototype systems installed in IKTS' SOFC laboratory (left) and at customer's site in Pune, India (right).
Figure 14. Overview of the initial characterization test with one of the h2e^® Proof-of-Concept prototype systems. Test procedure includes steady state operation at rated power output and scheduled part load operation for process analysis.
Figure 15. Part load characteristics of the h2e® Proof-of-Concept prototype system. Stack fuel utilization was kept constant at 80 % between 1.400 W_el and 800 W_el, and was reduced at lower power outputs to maintain desired HotBox temperatures.

Technology Readiness of SOFC Stacks - A Review

Figure 1. Generic boundary diagram of a SOFC system.
Figure 2. Sample views of CFY stack (left, mounted in handling device, footprint 15x13 cm), and eneramic® stack (right, with transport lock, footprint 7x7 cm).
Figure 3. Visualization of technical readiness for CFY stacks in three different market segments.
Figure 4. Visualization of technical readiness for eneramic® stacks in two market segments.
Figure 5. TRL evolution of the eneramic® stack technology platform over three years, 2012 - 2015.
Figure 6. Specific market prices in different market segments for SOFC systems.

High-Temperature Direct Fuel Cell Material Experience

Figure 1. FCE is an integrated fuel cell company, providing turn-key distributed power generation solutions.
Figure 2. 14.9MW DFC fuel cell park in Bridgeport, CT: Five 2.8MW plants with Organic Rankine Cycle (ORC)
Figure 3. DFC schematics: High electric efficiency resulting from synergistic heat and mass transfer
Figure 4. DFC cell construction employs appropriately specified stainless cell hardware and nickel-based electrodes: All are commercial commodity materials.
Figure 5. ∼lm² flexible and durable DFC matrix produced by FCE: Continuous tape casting process is employed.
Figure 6. Faster coarsening of DFC matrix α-Li AlO₂ at reducing anode side observed in accelerated cells.
Figure 7. Advanced matrix demonstrated significantly enhanced stability of pore structure.
Figure 8. Protective coating effective in eliminating DFC cathode current collector corrosion
Figure 9. Excellent corrosion resistance of DFC high-Cr stainless steel bipolar plate under dual-atmosphere condition after 15,000h field operation (plate thickness ∼250μm): A higher Cr content is more effective in mitigating dual-atmosphere corrosion.

Development of Highly-Efficient Energy Storage System Using Soled Oxide Electrolysis Cell

Figure 1. Conceptual scheme of hydrogen power storage system.
Figure 2. Conceptual configuration diagram of the SOEC/SOFC electrical power storage system.
Figure 3. Schematic diagram of a flat-tube type single cell.
Figure 4. I-V properties in both SOFC and SOEC mode of flat-tube single cell.
Figure 5. Steam utilization characteristics at the SOEC mode.
Figure 6. Hydrogen-producing properties.
Figure 7. High temperature heat storage unit capsules.
Figure 8. Temperature changes of NaCl and outside wall of the capsule in the heat cycle test.
Figure 9. Diagram of hydrogen power storage system.
Figure 10. Image for 5MWe-class hydrogen power storage system.
Figure 11. Specific electricity consumption for the hydrogen production.
Figure 12. Charge-discharge properties for SOEC/SOFC power storage system.

Thermoelectric Properties Higher Manganese Silicide Containing Small Amount of Mnsivsinano-Particles

Fig. 1 XRD data plotted for MnSi_γ with different composition γ =1.67, 1.73, 1.79, 1.81, and 2.11.
Fig. 2 SEM Images: (a), (b), and (c) shows microstructure of liquid quenched samples of γ=1 .67, 1.73, and 1.81 respectively, (d), (e) and (f) shows microstructure of SPS samples γ=l-67, 1.73, and 1.81, respectively.
Fig. 3: The composition dependence of Seebeck coefficient for LQ and SPS (MnSi_γ) samples at room temperature.
Fig. 4: The composition dependence of electrical resistivity for LQ and SPS (MnSi_γ) samples at room temperature.
Fig. 5: The composition dependence of power factor for LQ and SPS (MnSi_γ) samples at room temperature.
Fig. 6: The composition dependence of measured k_total, with estimated k_Laticeux, and K_ehctronios: (MnSi_γ) SPS samples
Fig. 7: The composition dependence of ZT for MnSiγ at room temperature.

Anomalous Temperature Gradient Innon-Maxwellian Gases

Figure 1. Maxwell-Boltzmann distribution at two elevations before renormalization (a) and after renormalization (b). The distributions indicate that the gas is isothermal with elevation.
Figure 2. Electrical carriers are assumed to be held in a slab of high-Z thermoelectric material and subjected to an electrical field.
Figure 3. Fermion energy distribution is the product of the Fermi-Dirac distribution and the density of states.
Figure 4. Ferrmon energy distribution as a product of the Ferrm-Dirac distribution and of the density of states, at low elevation (a) and at high elevation (b). The Fermi-Dirac distribution is shifted to the left by a potential (—e)V= E_F thereby affecting the Fermion distribution.
Figure 5. Fermion energy distribution at two elevations before renormalization (a) and after renormalization (b). The distributions indicate that the Fermions are not isothermal with elevation.

Thermophysical Property of Poly-Si Phonomc Crystals for Thermoelectrics

Figure 1. SEM images of (a) the whole suspended Si PnC nanostructure and (b) a 2D PnC nanostructure with circular holes aligned as a square lattice (a = 300 nm and r = 115 nm).
Figure 2. (a) Schematic of the-TDTR technique and cross section of the suspended structure, (b) Simulated temperature distribution at 15 μs after pulse heating a PnC structure with a = 300 nm and r = 115 nm.
Figure 3. TDTR signals for the unpatterned membrane and the single-crystalline Si PnC nanostructures (r = 73 nm, 115 nm, and 126 nm). The dots and solid lines represent experimental and simulated TDTR signals, respectively.
Figure 4. Measured thermal conductivities for a variety of radii in single-and polycrystalline Si PnC nanostructures.
Figure 5. TEM images of top view for (a) undoped, (b) p-doped, and (c) n-doped polycrystalline Si thin films, (d) Histogram of the grain size measured on the surface for each thin film.
Figure 6. (a, b) SEM images and schematic cross section of the Si PnC nanostructures (a = 300 nm and radius r = 110 nm) for the four probe measurement (c) Normalized simulated electric potential distribution.
Figure 7. Measured electrical conductivities (a) and thermal conductivities (b) for the p-doped and n-doped polycrystalline Si PnC nanostrucrures with a variety of hole radii at 295 K.
Figure 8. Power factor (a) and ZT(b) for the p-doped and n-doped polycrystalline Si PnC nanostructures with a variety of hole radii at 295 K.

The Potential of Maximal ZT-Value for Thermoelectric Materials of Mil ISi 19 HMS Phase by Calculating Electronic Structure

Figure 1. The experimental and calculated XRD patterns for HMS were shown in (a), (b) show SEM images obtained for sample prepared at the nominal compositions.
Figure 2. Band structure of Mn11Si19 (HMS). Several bands exist in the narrow energy range of a few hundred meV from both edge of the energy gap.
Figure 3. (a) and (b) represent Electronic density of states, N() and the normalized spectral conductivity, σ_normed(), for Mn₁₁Si₁₉ (HMS), respectively.
Figure 4. (a)Temperature dependence of chemical potential μ(7). (b) The electronic density of states N() together with μ(T) at T= 0 K, 300 K, 650 K and 1000 K.
Figure 5. The experimental Seebeck coefficient at temperature range from 300 K to 1000 K together with calculated Seebeck coefficient at the energy of μ(0 K) = 0 meV.
Figure 6. The experimental electrical resistivity and the calculated relaxation time of electron for HMS.
Figure 7. (a) The electron thermal conductivity κ_el^total were calculated by N() and σnormed() and τ(T) together with the first and second term in Eq.(3). (b) The calculated lattice thermal conductivity were calculated by κ_masured minus calculated κ_el.
Figure 8. A-factor (=S² T_ρ^-1κ_el-1)and B- factor = (1+κ1at/κel)^-1] were calculated by σ(T) andμ(T).

Development of Ga Doped Hollandites Ba_xCs_y(Ga_2x+yTi_8-2x-y)O₆ for Cs Immobilization

Figure. 1 XRD patterns of the synthesized hollandite containing different Cs levels with fixed A site occupancy of 1.33/2
Figure 2. Evolution of lattice parameters versus Cs content; experimental results are plotted in black, computation results are plotted in red.
Figure 3. Back scattered images of the sintered pallets at magnification of 300, a) Ba_1.16C_s0Ga_2.32Ti_5.68O₁₆; b) Ba_1.04Cs_0.24Ga_2.32Ti_5.68O₁₆; c) Ba_0.667Cs_0.667Ga₂Ti₆O₁₆. d) CSl.₃₃Ga_1.33Ti_6.67O_l6.
Figure 4. SEM-EDX elemental maps corresponding to the back-scattered images in Figure 3.

Atomistic Simulations of Ceramic Materials Relevant for Nuclear Waste Management:honey Cases of Monazlte and Pyrochlore

Figure 1. The Margules interaction parameters as a function of the endmembers volume mismatch for (Ln_1-x(Ln/An)xPO₄ (left) and MgThLn(PO₄) (right) solid solutions. In the left panel, circles and triangles represent the results for the solid solutions of (La_1-xLn_x)PO₄ and (La_1-xAn_x)PO₄, respectively. Square and diamond refer to the solid solutions of (Ce_1-xLn_x)PO₄ and (Sm_1-xLn_xPG₄. respectively. In the right panel, squares and circles represent the results for (Ln_1-2xMg_x Th_x)PO₄ and (_Ln_l-2_xCa_xTh_x)PO₄, respectively, the experimental data is shown are the small black point³⁷
Figure 2 The probability of defect formation in LaPO₄ for La PKA. The solid line is the fit obtained using Eq. (3).
Figure 4. The calculated CA DEFs and AFP DEFs for A₂Zr₂O₇, and A₂HF₂O₇ (A=La, Nd, Sm, Eu_: Gd,Y, Er,Yb and Lu).
Figure 1 Photographs of Zircaloy and SiC/SiC composite tubes.

Development of Joining Method for Zircaloy and SiC/SiC Composite Tubes by Using Fiber Laser

Figure 2 Photograph of experimental equipment for fiber laser irradiation.
Figure 3 Laser profile for fiber laser irradiation.
Figure 4 Photo of Zircaloy tubes after fiber laser irradiation.
Figure 5 Photo of Zircaloy - SiC/SiC composite joint with flat cutting.
Figure 6 SEM images of Zircaloy - SiC/SiC composite joint with flat cutting.
Figure 7 Photo of Zircaloy - SiC/SiC composite joint with screw cutting.
Figure 8 Digital microscope image of Zircaloy - SiC/SiC composite joint with screw cutting.
Figure 9 Digital microscope images of joint interface of Zircaloy - SiC/SiC composite joint with screw cutting.
Figure 10 SEM images of joint interface of Zircaloy - SiC/SiC composite joint with screw cutting.

An Investigation on the Cycle Performance of LiFePO₄ Pouch Cells by a Combination of Synchrotron Based X-ray Diffraction and Absorption Spectroscopy

Figure 1: Schematic diagram of a laminated pouch type 1.0 Ah cell.
Figure 2. Capacity retention vs. cycle number for the LFP/graphite cells cycled at different mole ratios of Fe/P.
Figure 3. XRD patterns of the cycled LiFePO₄ cathodes with different Fe/P mole ratios were performed at the 2 C/5 C charge/discharge rate in the fully charge state.
Figure 4. XRD patterns of the cycled graphite anodes corresponding to the LEP cathodes with different Fe/P mole ratios were performed at the 2 C/5 C charge/discharge rate in the fully charge state.
Figure 5. Water contents of samples A and B at different times in the air.
Figure 6. Specific surface areas of samples A and B at different times in the air.
Figure 7. Fe L,_3,2-edge spectra of samples A, B, and C.
Figure 8. The discharge curves of samples A and B of pouch cells at 1 C. Insert: The discharge curves of 2032 coin cells at 1 C.

The Influence of the Synthesis Route on Electrochemical Properties of Spinel Type High-Voltage Cathode Material LiNi_0.5Mn_1.5O₄ for Lithium Ion Batteries

Figure 1: SEM-images of LiNi_0.5Mn_1.5O₄ synthesized using different precursors: (a) sample 1, (b) sample 2.
Figure 2: Discharge capacity with different C-rates for cells using LiNi_0.5Mn_1.5O₄ as cathode material and metallic lithium as anode material. The discharge C-rates are indicated in the figure. All cycles where charged with the same C-rate as the respective discharge.
Figure 3: Second discharge curve of sample 1 and 2, respectively, at a C-rate of 0.1 C.

High Temperature Solar Receiver with Ceramic Materials

Figure 1: CSP technologies: actual market share and outlook, data from [1].
Figure 2: Solar tower power plant with open volumetric receiver technology: flow sheet (left) and demonstration plant Solar Tower Jülich in operation (right)
Figure 3: Principle of the volumetric absorber (left) and receiver surface covered with ceramic absorber modules (right).
Figure 4: Schematic view of power plant with pressurized volumetric receiver in combination with a tube receiver (left) and cluster of three PVR integrated in CESA 1 tower on Plataforma Solar de Amería (right)
Figure 4: Schematic of a PVR (left): pressure vessel (1), quartz window (2), inlet absorber (3). outlet absorber (4), secondary concentrator (5) and schematic of a receiver cluster (right)
Figure 5: Single ceramic module (left), cluster of modules with distributor and collector
Figure 6: Examples for receiver layout; left: small scale, only ceramic modules, right: large scale, serial with metallic tube receiver
Figure 7: Schematic of particle receiver system
Figure 8: Schematic view of falling particle receiver (left) and centrifugal receiver (right).
Figure 9: Distribution of flux density, mass flow rate and air outlet temperature for the design case of a cylindrical receiver (from [7]).
Figure 10: 2D and 3D plot of flux distribution on absorber, scale from 0 to 800 kW/m
Figure 11: 2D (left) and 3D plot (middle) of absorber temperatures, scale from 800 to 1300°C and fluid exit temperature (right), scale from 950 to l050°C
Figure 12: Workflow simple pre-design
Figure 13: Typical result of simplified simulation of ceramic module; temperature field (left), deformation (not true scale) and stresses (right).
Figure 14: Example result from parametric study

Determination of Parameters for Improved Efficiency in Thermal Energy Storage Using Encapsulated Phase Change Materials

Figure 1. Schematic of EPCM Capsule
Figure 2. The temperature at the center of the EPCM capsule for a 25 mm by 50 mm (diameter by height), 25 mm by 75 mm, 50 mm by 50 mm, and 50 mm by 75 mm capsule size along with the critical cooling rate for Na₄B₂O₅

Tuning the Spectral Selectivity of Sic-Based Volumetric Solar Receivers With Ultra-High Temperature Ceramic Coatings

Figure 1 : Normal spectral reflectivity acquired at room temperature for (1) ZrC, (2) TaC and (3) ZrB2. Modelled spectra with the help of Equation 1 and Equation 2 for (4) ZrC, (5) TaC and (6) ZrB₂
Figure 2 : Critical thicknesses beside which a dense and homogenous slab can be considered as optically thick (1) ZrC, (2) TaC and (3) ZrB₂.
Figure 3 : (a) 3D image of α-SiC open-cell foam (1 × 1 × 1 cm³) obtained with the iMorph software. Reconstructed α-SiC open-cell foam (1 ×1 × 1 cm³) with (b) 24 PPI, p = 49 %, (c) 24 PPI, p = 61 %, (d) 24 PPI, p = 81 % (e) 24 PPI, p = 96 %
Figure 4 : Normal spectral emittance of fictitious slabs of (1) ZrC, (2) TaC and (3) ZrB₂ and modelled emittance of an α-SiC open-cell foams internally coated with (4) ZrC, (5) TaC and (6) ZrB₂. The curve 7 depicts the normal spectral emittance of the α-SiC open-cell foam without coating.
Figure 5: Normalized distribution of the impacts undergone par rays during their travels within ZrB₂ open-cell foams (1 × 1 × 1 cm³, 24 PPI) with prescribed porosities: (1) p = 49 %, (2) p = 61 %, (3) p = 70 %, (4) p= 81 % and (5) p = 96 %. The wavenumber is 10000 cm^-1
Figure 6: Normalized distribution of the impacts undergone par rays during their travels within ZrB₂ open-cell foams (1 × 1 × 1 cm³, 24 PPI) with prescribed porosities: (1) p = 49 %, (2)p = 61 %, (3) p = 70 %, (4) p= 81 % and (5) p = 96 %. The wavenumber is 4000 cm^-1.
Figure 7 : Calculated effective emittances at T = 300 K of coated foams with growing porosities (from 49 % up to 96 %, 24 PPI, 1 × 1 × 1 cm³) for ω = 2000 cm^-1 (hollow symbols) and for ω = 20000 cm^-1 (filled symbols). The curves (1) and (2) corresponds to a coating composed of ZrC, (3) and (4) corresponds to a coating composed of TaC, (5) and (6) corresponds to a coating composed of ZrB₂. The curves (7) and (8) corresponds to α-SiC open-cell foams

Thermo-Mechanical Analysis of a Silicon Carbide Honeycomb Component Applied as an Absorber for Concentrated Solar Radiation

Figure 1. Photographs of the Jülich Solar lower (lelt), a part of a single absorber module and the solar receiver during installation
Figure 2. The simple and real geometries of the solar absorber
Figure 3. Cross-sectional view of the absorber with cell density 80cpsi (standard geometry) and 200cpsi (advanced geometry)
Figure 4. Schematic draws of the bending tests and theoretical equations for the calculation of the maximum stress in a dense material.
Figure 5. The air temperature in the channel (a) and the heat transfer coefficient (b) from one channel model COMSOT 3.5 for the standard channel (2:0,8mm)
Figure 6. The inlet heat flow density for the cloud-effect model
Figure 7. Maximum stress in the principal coordinate system for the double ring bend test for the 80cpsi (a) and for the 200cpsi sample (b)
Figure 8. The temperature fields at stationary homogeneous radiation from left to right: simple geometry, real geometry 80cpsi and real geometry 200cpsi.
Figure 9. Maximal stresses in the absorber (from left to right) with simple geometry (80 cpsi) and with real geometry (80cpsi and 200cpsi).
Figure 10. Temperature (a) and stress distribution (b) at the non-homogeneous radiation
Figure 11. Temperature distributions at stationary homogeneous radiation with additional temperature gradients in the diagonal (a) and in the axial direction (c). (b) and (d) show corresponding stresses.
Figure 12. The comparison of the maximum and minimal temperatures for both real structures
Figure 13. The temperature fields in the following time points from left to right: at start, 3s after the cooling start, 15s after the cooling start, 3s after the heating start, 15s after the heating start and at the end (30s after the heating start). The figures of the upper series belong to the simple geometry, the figures of the middle series to the real geometry with 80cpsi and the lower series to the real geometry with 200cpsi.
Figure 14. The stress distribution in the simple structure (upper line) and the increase of the maximum mechanical stress locations in the real geometry 80cpsi of the solar absorber at the 4 intermediate time points mentioned above (from left to right).
Figure 15. Comparison between the fracture stress and the maximum mechanical stress during the cloud-effect simulation (left) and the maximum mechanical stress as a function of the maximum temperature difference (right).

Anomalous Proximity Effect and More Than one Majorana Fermion

Figure 1. Schematic image of the zero energy states at two edges of an isolating p_x-wave superconductor. The number of the MBSs at either edge is equal to N_c. All of the MBSs at the left (right) edge have λ =1 (λ =+1)
Figure 2. Schematic picture of the NS junction of a p_x-wave superconductor
Figure 3. Differential conductance is plotted as a function of the bias voltage for several length of disordered segment L.

Atomic-Scale Study of the Superconducting Proximity Effect in Manganite/Cuprate Thin-Film Heterostructures

Figure 1: Schematic illustration of long-ranged proximity effect across a superconductor/ ferromagnet junction. Odd-frequency spin-triplet pairs with even-parity orbital symmetry are induced near the interface and penetrate into the ferromagnet far deeper than spin-singlet pairs, since spin-triplet pairs are not easily broken by the exchange field in the ferromagnet.
Figure 2: The lattice structures of YBCO-123, YBCO-124 and YBCO-247, with the Cu, Y, and Ba atoms color-labeled as yellow, green, and red, respectively. The CuO chain sites are labelled as S and D for single-chains and double-chains respectively.
Figure 3: Scanning tunneling conductance spectra measured with a Pt-Ir tip on thin-film samples at 4.2 K. Panel (a) shows spectra taken on bilayer LCMO/YBCO films, for 10-nm (blue curve) and 20-nm (red curve) LCMO thickness. These spectra are distinct from data taken on a unilayer YBCO film (b), but similar to data taken on a unilayer LCMO film (c).
Figure 4: High-resolution HAADF-STEM image of a 25-nm/50-nm bilayer LCMO/YBCO film grown on (OOl)-oriented LSAT substrate. Blue dotted line indicates the LCMO/YBCO interface, and the Cu, Y, and Ba atoms are respectively color-labeled as yellow, green and red. While the YBCO layer nominally has 123 stoichiometry, the intergrowths of double-CuO chains effectively form nanoscale YBCO-247 regions.
Figure 5: Comparison between bilayer LCMO/YBCO and unilayer YBCO films. Panel (a) shows the STEM image of a bilayer film: nanoscale YBCO-247 regions appear throughout the YBCO layer, with the double-CuO chains indicated by arrows. These double-CuO intergrowths are largely absent in a unilayer YBCO film, as shown in panel (b). The peak locations in the XRD patterns for the bilayer film (panel c) and for the unilayer film (panel d) are indistinguishable. Note that the nanoscale YBCO-247 regions appearing in the bilayer film do not appear in the XRD data within the resolution of our instrument.
Figure 6: Plot of normalized resistance vs. temperature for unilayer YBCO and bilayer LCMO/YBCO films. All the unilayer films show sharp superconducting transitions with T_c near 90 K. The 25-nm/25-nm bilayer LCMO/YBCO film shows a broadened and reduced T_c near 60 K. The inset shows a schematic diagram illustrating the differences in both lattice symmetry and lattice parameters of the ab-plane lattice structure between YBCO-123, YBCO-247, LCMO, and LSAT. In the diagram, the relative length scales between the a- and b-axes for each material, and between the materials, are exaggerated for clarity.
Figure 7: Plot of normalized resistance vs. temperature for trilayer LNO/YBCO/LNO and unilayer YBCO films grown on (00l)-oriented STO substrates. In the trilayer, YBCO is sandwiched between two LNO layers, each 25 nm thick, to symmetrize the heteroepitaxial strain. At 25 nm YBCO thickness, the trilayer film has a T_c ∼ 60 K, which is much lower than that of the unilayer YBCO film. The inset shows similar behavior at 12.5 nm YBCO thickness, with data from trilayer LCMO/YBCO/LCMO included for comparison: superconductivity onsets at similarly low temperatures (∼45K) for both LNO/YBCO/LNO and LCMO/YBCO/LCMO, as compared with unilayer YBCO.

Tunneling and Photoemission Spectra in Cuprate Superconductors:honey Evidence for Strong Multiple-Phonon Coupling and Polaronic Effects

Figure 1. a) d²I/dV² spectrum for an electron-doped PLCCO sample with T_c = 21 K, which is reproduced from Ref.³² b) d²I/dV² spectrum for an electron-doped PLCCO sample with T_c = 24 K, which is reproduced from Ref.³⁰ The energy positions of the d²I/dV² spectra are measured from their superconducting gaps.
Figure 2. d²I/dV² spectrum at 7.2 K for a hole-doped La_1.84Sr_0.16CuO₄ with T_c = 24 K, which is reproduced from Fig. 4 of Ref. ²⁹. The energy position of the d²I/dV² spectrum is measured from the superconducting gap.
Figure 3. a) d²I/dV² spectrum of bi-layer hole-doped Bi₂Sr₂CaCu₂O_s+y.The d²I/dV² spectrum is obtained by numerically taking the derivative of the dI/dV spectrum of Ref.³⁹ after the spectrum is smoothened by cubic spline. The energy position of the d²I/dV² spectrum is measured from the superconducting gap. b) Phonon density of states for slightly overdoped Bi₂Sr₂CaCu₂O_s+y. The curve is reproduced from Ref.⁴⁰
Figure 4. a) Dependence of E_dip-E_pk on T_c, which is reproduced from Ref.¹⁰ The E_dip-E_pk values were determined from ARPES data, b) Dependence of E_dip-E_pk on the superconducting gap. The E_dip-E_pk values are obtained from Supplementary Figure 2 of Ref.⁴⁹ The different E_dip-E_pk values extracted from ARPES and tunneling data may arise from different energy resolutions that affect peak width.
Figure 5. Doping dependence of the energy position of the peak and hump features of the angle-resolved photoemission spectra along the antinodal direction. The data were reproduced from Ref.⁵⁵
Figure 6. a) The peak-hump energy separations in the ARPES of BSCCO, which are evaluated from the data in Fig. 5. b) Dependence of the peak-hump energy separation on 1/g² in SIN tunneling spectra (similar to ARPES), which is predicted from a lattice polaronic model where 72-meV phonon modes are involved in polaron formation.
Figure Al. The calculated tunneling conductance dI/dV for a superconductor-insulator-normal (SIN) junction based on the polaron-bipolaron theory of superconductivity. The numbers in the figure are the g² values.
Figure A2. a) Scanning tunneling spectrum of optimally doped Bi-2223. b) The calculated scanning tunneling spectrum based on polaronic superconductivity. The parameters for the calculation are listed in the figure. The measured SIN spectrum was reproduced from Ref. ⁶⁶
Figure A3. The symmetrized energy distribution curves (EDCs) along the diagonal direction for slightly overdoped Bi-2212 and Bi-2223. The data are taken from Refs. ^76,77 The dip feature at zero energy proves a finite gap.

Preface

The global challenges we face require innovative thinking and sustainable technology to meet increased demands for energy, clean water, and infrastructure. Research of materials —specifically, ceramic materials —continues to provide solutions to everyday challenges such as environmental protection, energy supply and generation, and healthcare. The 11th International Symposium on Ceramic Materials and Components for Energy and Environmental Applications (11th CMCEE), held June 14-19, 2015 at the Hyatt Regency Vancouver in Vancouver, B.C., Canada, identified key challenges and opportunities for ceramic technologies to create sustainable development.

This Ceramic Transactions volume contains papers submitted from the following six symposia held in Track 1: Ceramics for Energy Conversion, Storage, and Distribution Systems:

High-Temperature Fuel Cells and Electrolysis
Ceramic-Related Materials, Devices, and Processing for Heat-to-Electricity Direct Conversion
Material Science and Technologies for Advanced Nuclear Fission and Fusion Energy
Advanced Batteries and Supercapacitors for Energy Storage Applications
Materials for Solar Thermal Energy Conversion and Storage
High-Temperature Superconductors: Materials, Technologies, and Systems

After a peer-review process, 25 papers were accepted for inclusion in this proceedings volume. 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 also acknowledge the skillful organization and leadership of the meeting chairs, Mrityunjay Singh, Tatsuki Ohji, and Alexander Michaelis.

We hope that this proceedings will serve as a useful resource for the researchers and technologists in the field of energy conversion, storage, and distribution systems.

THOMAS PFEIFER, Fraunhofer Institute for Ceramic Technologies and Systems —IKTS, German

JOSEFMATYÁŠ, Pacific Northwest National Laboratory, USA

PALANI BALAYA, National University of Singapore, Singapore

DILEEP SINGH, Argonne National Laboratory, USA

JOHNWEI, University of Toronto, Canada

Ceramics for Energy
Conversion, Storage,
and Distribution Systems

Ceramic Transactions, Volume 255

A Collection of Papers Presented
at CMCEE-11,
June 14-19, 2015,
Vancouver, BC, Canada

Preface

HIGH-TEMPERATURE FUEL CELLS AND ELECTROLYSIS