Processing, Properties, and Design of Advanced Ceramics and Composites II

Ceramic Transactions, Volume 261

Edited by

Narottam P. Bansal

Ricardo H. R. Castro

Michael Jenkins

Amit Bandyopadhyay

Susmita Bose

Amar Bhalla

J.P. Singh

Morsi M. Mahmoud

Gary Pickrell

Sylvia Johnson

This edition first published 2017
© 2017 The American Ceramic Society

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Library of Congress Cataloging-in-Publication Data is available
ISBN: 9781119423805
ISSN: 1042-1122

Cover design by Wiley

Contents

Preface

ADVANCES IN COMPOSITES

The Effect of Paste Water Content on the Green Microstructure of Extruded Titanium Dioxide
1. Mustafa Kanaan Alazzawi and Richard A. Haber
Compaction Plasticity of Spray Dried Alumina Granules to Form Microstructural Uniformity and Green Strength
1. I. P. Maher and R. A. Haber
A Model for the Numerical Simulation of Liquid Silicon Infiltration into Porous Carbon/Carbon Preforms
1. Khurram Iqbal, Sudhanshu Dwivedi, and Stevens Cadet
Foreign Object Damage in a SiC Fibrous Composite
1. Nesredin Kedir, David Faucett, Luis Sanchez, and Sung R. Choi

INTERNATIONAL STANDARDS FOR PROPERTIES AND PERFORMANCE OF ADVANCED CERAMICS

ASTM Subcommittee C28.01 Mechanical Properties and Reliability
1. Michael G. Jenkins
ASTM Committee C28: International Standards for Properties and Performance of Advanced Ceramics-Three Decades of High-Quality, Technically-Rigorous Normalization
1. Michael G. Jenkins and Jonathan A. Salem
ASTM Subcommittee C28.07 Ceramic Matrix Composites
1. Michael G. Jenkins and Andrew Wereszczak
Activities in ISO/TC206 Fine Ceramics—A Quarter Century of Progress
1. Shuji Sakaguchi

SINTERING AND RELATED POWDER PROCESSING

The Usage of Heat Explosion to Synthesize Intermetallic Compounds and Alloys
1. Karina Belokon and Yuriy Belokon
Structural Characterization of Carbon-Based Materials Obtained by Spark Plasma Sintering of Non-Graphitic Carbon with Nickel and Iron as Catalysts and Space Holders
1. A. V. Ukhina, B. B. Bokhonov, D. V. Dudina, K. Yubuta, and H. Kato
On the Effect of Electric Field during Spark Plasma Sintering—A “Faraday Cage” Approach
1. Anil Prasad, Somi Doja, and Lukas Bichler
Enhancement of Diffusion Bonding of Silver Graphite to Copper by Severe Plastic Deformation
1. Daudi R. Waryoba

SURFACE PROPERTIES OF BIOMATERIALS

Hydroxyapatite Precipitation on Ti-6Al-4V and Ti-6Al-7Nb Alloys: Effect of Surface Conditions
1. Mahmoud Abdel-salam, Waleed Khalifa, and Shimaa El-Hadad
Microstructure and Mechanical Properties of Heat Treated Ti-6Al-7Nb Alloy
1. Ahmed Fityan, Shimaa El-Hadad, and Waleed Khalifa
Surface Modification of Titanium Foams Produced by Freeze-Casting
1. Silvia Briseño Murguia, Joshua Barclay, Samir M. Aouadi, and Marcus L. Young
The Effect of Plastic Deformation on the Cell Viability and Adhesion Behavior in Metallic Implant Materials
1. B. Uzer and D. Canadinc

INNOVATIVE PROCESSING

Influence of Hot-Pressing Time on Phase Evolution of SHS Obtained Ti₂AlC Active Precursor Powder
1. L. Chlubny, J. Lis, P. Borowiak, and K. Chabior
Increasing the Silicon Carbide Content in Laser Sintered Reaction Bonded Silicon Carbide
1. Sebastian Meyers, Lien De Leersnijder, Jef Vleugels, and Jean-Pierre Kruth
Challenges in Spark Plasma Sintering of Cerium (IV) Oxide
1. Anil Prasad, Linu Malakkal, Lukas Bichler, and Jerzy Szpunar

DIELECTRIC MATERIALS AND ELECTRONIC DEVICES

Study of the Dielectric Response of Rare-Earth Modified PZT Ferroelectric Ceramics—An Approach to the Diffuse Phase Transition
1. S. P. Hessel, A. C. Silva, R. Guo, A. S. Bhalla, and J. D. S. Guerra
Influence of Processing and Microstructure on Dielectric Properties of Calcium Copper Titanate Ceramics
1. Disna P. Samarakoon, Nirmal Govindaraju, and Raj N. Singh
Effect of A-Site Doping by La, Ba, and Ca on Thermoelectric Properties of Sr₂FeTiO₆ Double Perovskites
1. P. Roy and T. Maiti

PROCESSING AND PERFORMANCE OF MATERIALS USING MICROWAVES, ELECTRIC, AND MAGNETIC FIELDS

Change of Energy Transfer Medium from High Temperature Gas to Microwave
1. Kazuhiro Nagata and Motoyasu Sato
Effect of Laser Shock Peening (LSP) on AISI L6 Hot Work Tool Steel
1. Sachin Patil, Valmik Bhavar, Prakash Kattire, P. P. Date, and Rajkumar Singh
Comprehending Microwave-Enhanced Isothermal Process Kinetics in Ceramic Processing
1. Boon Wong

THERMAL PROTECTION MATERIALS AND SYSTEMS

Characterization of Deposits Found on Carrier Panel Tiles Recovered from the Space Shuttle Columbia
1. Brenda R. Arellano, Stephen W. Stafford, Darren M. Cone, and Mayra Contreras
Unlocking the Thermal Protection Potential of Ceramic Matrix Composites
1. R. Cook
Determination of the Mechanical Properties of the Lightweight Ablative Material ZURAM
1. Thomas Reimer, Christian Zuber, Jakob Rieser, and Thomas Rothermel

ADVANCED MATERIALS FOR HARSH ENVIRONMENTS

In Situ TEM Observations of Corrosion in Nanocrystalline Fe Thin Films
1. David Gross, Josh Kacher, Jordan Key, Khalid Hattar, and Ian M. Robertson
Removal and Separation of Metal Ions from the Chromium Plating Wastewater using Persimmon Gel and Immobilized Microbe
1. Takehiko Tsuruta and Tomonobu Hatano

ZIRCONIA BASED MATERIALS

Microstructural Evolution and Tribocorrosion Performance of Novel Laser Clad Ti-Ni-ZrO₂ Composite Coatings in 3.5% NaCl Solution
1. Babatunde A. Obadele, Oladeji O. Ige, and Peter A. Olubambi
The Evolution of the Structure and the Transport Properties of ZrO₂-Y₂O₃, ZrO₂-Sc₂O₃ and ZrO₂-Y₂O₃-Sc₂O₃ Crystals, Obtained by Skull Melting Technique
1. M. A. Borik, S. I. Bredikhin, V. T. Bublik, A. V. Kulebyakin, I. E. Kuritsyna, E. E. Lomonova, F. O. Milovich, V. A. Myzina, V. V. Osiko, P. A. Ryabochkina, S. V. Seryakov, and N. Yu. Tabachkova

CONTROLLED SYNTHESIS, PROCESSING, AND APPLICATIONS OF STRUCTURAL AND FUNCTIONAL NANOMATERIALS

Preparation and Characterization of Poly (Meta-Phenylene Isophthalamide) Microporous Membranes by Coaxial Electrospinning
1. Weiwang Chen and Wenguo Weng
Molecular Dynamics Simulations of Glancing Angle Deposition of Polymer Nanoparticles
1. David A. Kessler and Marriner H. Merrill

CERAMIC OPTICAL MATERIALS

Highly Translucent, High Strength Zirconia Ceramics with Nano-Sized Tetragonal Domain
1. Isao Yamashita, Yuya Machida, and Shouichi Yamauchi

MULTIFUNCTIONAL OXIDES

Physical Property Relationships in Spinel Ferrite Thin Films Developed Using the Spin-Spray Deposition Method
1. N. M. Ray, W. T. Petuskey, H. Lorzel, and M. R. McCartney

EULA

List of Tables

Table 1
Table 2

Table I
Table II

Table 1

Table I
Table II
Table III
Table IV

Table I
Table II
Table III
Table IV
Table V
Table VI

Table I
Table II
Table III
Table IV

Table I
Table II
Table III
Table IV
Table V

Table I
Table II

Table I
Table II

Table 1

Table 1
Table 2

Table I
Table II

Table I

Table I
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Table I
Table II

Table 1

Table I

Table 1

Table 1

Table 1
Table 1

Table I
Table II
Table III

Table I

Table 1

Table 1
Table 2
Table 3
Table 4
Table 5
Table 6
Table 7
Table 8
Table 9
Table 10
Table 11

Table 1

Table I
Table II
Table III
Table IV

Table I

Table 1

List of Illustrations

Figure 1. A typical mixing profile shows the mixing regions.
Figure 2. A typical extrusion profile shows the extrusion regions.
Figure 3. Schematic shows the top geometry (PU25) and the stationary geometry (PL25) of Kinexus rotational rheometer.
Figure 4. A typical Kinexus rotational rheometer profile for green strength measurement.
Figure 5. A degradation behavior of the binder within the extrudate.
Figure 6. Schematic shows the direction of scanning from the edge toward the center of the extrudate’s cross-section.
Figure 7. (a) The mixing torque of the low H₂O vs the high H₂O for the low binder mixture, (b) The mixing torque of the low H₂O vs the high H₂O for the high binder mixture.
Figure 8. Mixing profiles of a water range (50.0-56.4%). (a) Low binder and, (b) High binder.
Figure 9. (a) Extrusion pressure of the low H₂O vs the high H₂O for the low binder paste. (b) Extrusion pressure of the low H₂O vs the high H₂O for the high binder paste.
Figure 10. (a) The green strength of the low H₂O vs high H₂O for the low binder extrudate, (b) The green strength of the low H₂O vs high H₂O for the high binder extrudate.
Figure 11. SEM images of the extrudate cross section of low and high water with the low binder (LWLB) and (HWLB), respectively. Also, the extrudate cross section of low and high water with high binder (LWHB) and (HWHB) binder, respectively at low magnification.
Figure 12. The distribution of porosity from the edge towards the center of extrudates as determined using the ImageJ software on infiltrated and polished sections. (a) Low H₂O vs high H₂O for the low binder extrudate, (b) Low H₂O vs high H₂O for the high binder extrudate
Figure 13. SEM images of (HWLB), (LWLB), (HWHB), and (LWHB) extrudates at 10000x magnification.

Figure 1. (a) Example of a compaction curve showing the different stages during compaction. (b) A schematic of the compaction die used with the Instron compressive tester.
Figure 2. Plot shows both curves for low and high binder granules compacted using different particle size distributions superimposed on the same plot for comparison.
Figure 3. SEM Heat Treatment difference shown between (a) 150°C heat treatment held for 2 hours and (b) 500°C heat treatment held for 2 hours. Both samples were low binder PVA granules pressed at a pressure of 5 MPa.
Figure 4. SEM microstructure images of (a) low PVA binder and (b) high PVA binder pressed alumina samples at a pressure of 7 MPa, roughly 40 – 45% dense using the 150°C heat treatment.
Figure 5. SEM microstructure images of (a) low PVA binder and (b) high PVA binder pressed alumina samples at a pressure of 100 MPa, roughly 60 – 65% dense using the 150°C heat treatment.

Figure 1. A schematic diagram of liquid silicon infiltration (LSI) process, and the process involves in infiltration of carbon fiber preforms with molten Si.
Figure 2. Schematic view of the (a) siliconization experimental setup, and the capillary-rise configurations (b) at an angle of β = β and (c) β = 0 degrees.
Figure 3. Theoretical Si system infiltration profiles in capillaries of initial radii (r₀ = 10 μm in (a) and r₀ = 15 μm in (b)) at the temperatures of 1723, 1773, 1823, 1873 and 1923 K.

Figure 1. Typical microstructure of the fibrous SiC composite.
Figure 2. A typical SEVBN specimen geometry used for fracture toughness testing
Figure 3. Experimental setups for FOD and flexure testing.
Figure 4. Vickers indentations on the fibrous SiC composite at various indent loads.
Figure 5. Vickers hardness (HV) as function of indent force (P) of the fibrous SiC composite
Figure 6. SEM micrograph of the failed SEVNB surface.
Figure 7. Summary of impact damage morphology generated on the fibrous SiC composite target (front-side) and back-side) and 1.59 mm diameter projectile (top-view and side-view)
Figure 8. SEM micrographs showing cross-sections of impact damage in the composite.
Figure 9. Representative force-vs-deflection curves for the fibrous SiC composites impacted by 1.59 mm steel ball projectiles and tested in four-point flexure configuration. The flexure response of the as-received (As-R) specimen is also provided.
Figure 10. Results of post-impact strength as a function of impact velocity for a fibrous SiC composite impacted by 1.59 mm steel ball projectiles. The solid lines represent the best-fit. The “As-R” denotes the as-received strength of the material.
Figure 11. Representative SEM micrographs of the fracture regions for as-received and impacted specimens tested in four-point flexure.

Figure 1-Range of test specimens and test configurations in Test Method C1161 [17]
Figure 2-Articulating test fixture for flexure testing advanced ceramics
Figure 3-Examples of the Variety of Tensile Test Specimens from Test Method C1273 [20]
Figure 4-Primary Test Specimen and Fixture Configurations (all dimensions in mm) allowed in Test Method C1421 [22]
Figure 5-Fracture toughness of window material for different crystallographic planes [29]
Figure 6 – Comparison of biaxial flexural strength for two window materials [29]

Figure 1 – Timeline for the first three decades of ASTM Committee C28
Figure 2 – Membership of ASTM Committee C28 from 1986 to 2016
Figure 3 – Front page of Advanced Ceramic Sentinel used for outreach
Figure 4 – Pictorial illustrations of Committee C28 standards
Figure 5 – Cumulative number of Committee C28 standards and number of standards needing mandatory review in any given year
Figure 6 – Example of Mg-PSZ surgical implant
Figure 7 – Examples of silicon nitride rolling elements http://www.ortechceramics.com/product-category/ceramic-bearings/
Figure 8 – Fracture toughness of window material for different crystallographic planes [30]
Figure 9 – Comparison of biaxial flexural strength for two window materials [30]

Figure 1 – Range of test specimens and test configurations in Test Method C1275 [17]
Figure 2 – Interpretation of stress-strain curves to standardize terms and behavior [18].
Figure 3 – Example of Transthickness Tensile Test Arrangement from Test Method C1468 [19]
Figure 4 – Schematic of axially-loaded elastomer insert for tensile hoop strength test from Test Method C1819 [20]
Figure 5 – Test specimen geometries used in round robin programme (dimensions in mm) [27]
Figure 6 – Statistically-significant results from round robin programme [27]
Figure 7 – Interface of CMH-17 Statistical Analysis Program for A-basis and B-basis values [31]
Figure 8 – High temperature gas cooled reactor targeted for SiC-SiC CMCs addressed in the ASME Boiler and Pressure Vessel Code [32, 35]

Figure 1 - Stages for the development on ISO standards [4]
Figure 2 - Number ISO/TC206 standards published by year

Figure 1. Operating Temperature dependence of the reaction time in the thermal flow autoignition powder mixture Ti-Al
Figure 2. Thermodynamic analysis of formation γ-TiAl alloy
Figure 3. The results of microstructural analysis of the obtained titanium aluminides
Figure 4. The results of microprobe analysis of γ-TiAl alloy

Figure 1. XRD patterns of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cnd mixtures.
Figure 2. Raman spectra of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cnd mixtures.
Figure 3. SEM images of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cnd mixtures at 800°C (a) and 1000°C (b), holding time 3 min.
Figure 4. TEM images of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cnd mixtures at 800°C (a) and 1000°C (b), holding time 3 min.
Figure 5. XRD patterns of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-C_am mixtures at 500-1000°C, holding time 10 min.
Figure 6. Raman spectra of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-C_am mixtures at 500-1000°C, holding time 10 min.
Figure 7. SEM images of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cam mixtures at 600°C (a) and 1000°C (b).
Figure 8. TEM images of the carbon-based materials obtained by selective dissolution of nickel from the compacts Spark Plasma sintered from the Ni-Cam mixtures at 600°C (a) and 1000°C (b).
Figure 9. XRD patterns of the compacts Spark Plasma sintered from the Fe-C_am mixtures at 600-900°C, holding time 5 min, after iron has been (partially) dissolved.
Figure 10. Raman spectra of the compacts Spark Plasma sintered from the Fe-C_am mixtures at 600-900°C, holding time 5 min, after iron has been (partially) dissolved.

Figure 1 Working principle for Faraday cages.
Figure 2 Die set-up for electric field void SPS.
Figure 3 Particle Size Distribution for raw ZnO powder over 20 repeated trails.
Figure 4 Raw ZnO powder
Figure 5 Grain size distribution for pellets with and without Faraday cage
Figure 6 a) Microstructure of ZnO pellet without Faraday cage b) Microstructure of ZnO pellet with Faraday cage
Figure 7 Magnified microstructural images of a) pellet without Faraday cage b) Feature A c) Feature B and d) Feature C

Figure 1: (a) Schematic illustration of the ECAP processing through the 90° die, and (b) corresponding sample coordinates.
Figure 2: Particle size distribution for AgC and copper powders used for fabricating electrical contacts
Figure 3: Illustration of the filling and compaction process (a) initial filling, (b) initial compaction, (c) second filling, (d) second compaction, and this is repeated until the tube is ¾ filled. Foil removed before compaction.
Figure 4: Illustration of the change in the activation energy with ECAP processing
Figure 5: SEM micrographs of the AgC-Cu bilayer contact fabricated by the conventional press and sinter process showing (a) the diffusion layer and (b) graphite deposits at the interface.
Figure 6: SEM micrograph of the AgC-Cu contact showing the X-ray line scan across the interface. The white arrow shows the peak of graphite
Figure 7: SEM micrographs of the ECAPed AgC-Cu bilayer contact showing the X-ray line scan across the interface.
Figure 8: Phase ID maps of the (a) CPS processed and (b) ECAPed bi-layered specimens. The dark regions are either pores or graphite areas.
Figure 9: (100) IPF maps of the (a) CPS processed and (b) ECAPed bi-layered specimens
Figure 10: Grain boundaries showing orientation relations (ORs) between copper and silver in (a) CPS processed and (b) ECAPed bi-layered specimens.
Figure 11: Illustration of the (a) Cube-on-cube OR, (b) Oct-cube OR, and (c) Twin orientation relationship. The blue and red-hatched spheres represent A and B lattice, respectively.
Figure 12: Grain boundary structure of (a) silver grains, and (b) copper grains in the CPS processed sample.
Figure 13: Grain boundary structure of (a) silver grains, and (b) copper grains in the ECAPed processed sample.

Figure 1 SEM micrographs showing the general view of the forged specimen surfaces after immersion in hank solution: a) T64, 4 weeks immersion, (b) T67, 4 weeks immersion, (c) T64, 8 weeks immersion, and (d) T67, 8 weeks immersion.
Figure 2 pH variations during immersion in Hank solution.
Figure 3 SEM micrographs showing higher magnification and EDS analysis of the deposited surface layers: a) forged Ti64, (b) forged Ti67, (c) cast Ti64 and (d) cast Ti67 after 4 weeks immersion.
Figure 4 The general view of the forged specimens a) T64 and (b) T67 after 2 weeks immersion at RT, (c) T64 and (d) T67 after immersion at 2°C for 2 and 8 weeks respectively.
Figure 5 pH levels for the immersion in hank solution: (a) at room temperature, and (b) at 2°C.
Figure 6 pH levels in the Hank solution as a function of immersion time of forged Ti64 and Ti67. The specimens were oxidized in muffle furnace at 300, 500, and 700°C.
Figure 7 Forged-oxidized specimens after immersion for 4 weeks in Hank Solution. (a) Ti64, 300°C, (b) Ti67, 300°C, (c) Ti64, 500°C, (d) Ti67, 500°C, (e) Ti64, 700°C, (f) Ti67, 700°C.
Figure 8 Forged-oxidized specimens after immersion for 4 weeks in Hank Solution. a) Ti64, 500°C, b) Ti67, 500°C, c) EDS of Ti64, 500°C, and d) EDS of Ti67, 500°C.
Figure 9 pH levels in the Hank solution as a function of immersion time of cast Ti64 and Ti67 alloys, oxidized at 300, 500, and 700°C.
Figure 10 Cast oxidized specimens after immersion for 4 weeks in Hank Solution. (a) Ti64, 300°C, (b) Ti67, 300°C, (c) Ti64, 500°C, (d) Ti67, 500°C, (e) Ti64, 700°C, (f) Ti67, 700°C.
Figure 11 Cast oxidized specimens after immersion for 4 weeks in Hank Solution. (a) Ti64, 500°C, (b) Ti67, 500°C, (c) EDX of Ti64, 500°C, and (d) EDX of Ti67, 500°C.

Fig. 1 Pin on disk wear test
Fig. 2 Differential Scanning Calorimetry of the as-received Ti-6Al-7Nb samples.
Fig. 3 Optical micrograph of the a) as forged, b) b1 and c) b2 samples.
Fig. 4 Optical micrograph of the water quenched sample, b2, and showing the microstructural interface between the edge and the core of the sample.
Fig. 5 Optical micrograph of the double solution treated samples, a) b3, b) b4, c) b5and d) b6.
Fig. 6 Micrograph of the aged samples, a) b7, b) b8, c) b9 and d) b10.
Fig. 7 Hardness of the reference sample and the heat treated samples.
Fig. 8 Wear resistance expressed as friction coefficient, of the investigated samples.
Fig. 9 Worn surface (3D) of a) Ref., b) b1 (SST-AC) and c) b2 (SST-WQ) samples

Figure 1: SEM images of commercial Ti powder used in the study at two different magnifications (a-b).
Figure 2: SEM images of the cross-section of the Ti foam produced by freeze-casting at four different magnifications (a-d).
Figure 3: Ti foam with and without hydrothermally grown TiO2 nano-scaffolds using different synthesis conditions: a) 10M NaOH, 0.025g of TiO2 powder, 5hr furnace time. b) 2M NaOH, 0.01g of TiO2 powder, 3hr furnace time c) 10M NaOH, 0.03g of TiO2 powder, 4.5hr furnace time. d) 7.5M NaOH, 0.025g of TiO2 powder, 4hr furnace time. e) 5M NaOH, 0.025g of TiO2 powder, 5hr furnace time. f) Control Ti foam sample. No treatment.
Figure 4: SEM images of Ti foam with and without hydrothermally grown TiO2 nano-scaffolds using different synthesis conditions. a) 10M NaOH, 0.025g of TiO2 powder, 5hr furnace time. b) 2M NaOH, 0.01g of TiO2 powder, 3hr furnace time c) 10M NaOH, 0.03g of TiO2 powder, 4.5hr furnace time. d) 7.5M NaOH, 0.025g of TiO2 powder, 4hr furnace time. e) 5M NaOH, 0.025g of TiO2 powder, 5hr furnace time. f) Control Ti foam sample. No treatment.

Figure 1. X-ray diffraction pattern of the 316L stainless steel.
Figure 2. SEM images of the (a) undeformed and (b) 35% deformed 316L stainless steel samples.
Figure 3. AFM images of the sample deformed up to 35% strain captured with (a) 3D image and (b) amplitude error channel. The bottom image (c) represents the line profile obtained from the twinned region.
Figure 4. (a) Laser (b) and height images (topographic representations of the surface heights) of the slip lines within a grain in the sample deformed to 35% strain. (c) The line profile shows the step- like increase of the surface height by the slip lines within the region marked in (a) and (b). The color bar shows the surface roughness defined in terms of peak distance values along the normal to the surface (in μm).
Figure 5. CLSM images of the brain tumor cells seeded on the (a) undeformed and (b) 35% deformed stainless steel sample.
Figure 6. SEM images of the (a) brain tumor and (b) fibroblast cells on the stainless steel samples deformed up to 60%.
Figure 7. Fluorescent microscopy images of the brain tumor cells seeded on the 316L stainless steel undeformed sample (a), and those deformed up to 35% (b) and 60% (c).

Figure 1. XRD pattern of the Ti2AlC powders obtained by SHS reaction
Figure 2. XRD pattern of the Ti2AlC sample hot-pressed for 1 hour at 1100°C

Figure 1: Process chain for production of RBSC parts via laser sintering.
Figure 2: SiC (Carborex BW F320, left) and Si (Keyvest Simet 985, right) starting powders.
Figure 3: Phenolic resin impregnation approaches.
Figure 4: Angle of repose and avalanche angles for the Si-SiC powder blends.
Figure 5: Post laser sintering part density for different powder blends as a function of the laser energy density.
Figure 6: thermo-gravimetric analysis of the (pure) resol phenolic resin.
Figure 7: Optical micrograph of a part with a SiC content of 76%.
Figure 8: a gear (left) and extrusion head (right) in laser sintered Si-SiC.

Figure 1 Spark plasma sintering die set-up for electric current insulation
Figure 2 Raw Ceria powder
Figure 3 Stereo macrograph of Ceria pellet cross section sintered at 1400°C
Figure 4 Ceria pellet sintered at 1400°C with alumina encapsulation
Figure 5 Corroded edge of positive punch
Figure 6 X-ray diffractograms of ceria powders and SPSed pellets
Figure 7 The cross section of cerium dioxide pellet after sintering. The red arrows represent the possible path of oxygen ion mobility.

Figure 1. X-ray diffraction patterns for the powdered ceramic samples. The peaks were indexed according to the ICDD 46-0336 crystallographic data.
Figure 2. Images obtained by scanning electron microscopy (SEM) for the studied samples.
Figure 3. Temperature dependence of the real component of the dielectric permittivity (ε’), at various frequencies, for the studied samples.
Figure 4. Temperature dependence of the imaginary component of the dielectric permittivity (ε″), at various frequencies, for the studied samples.
Figure 5. Temperature dependence of the converse dielectric permittivity for the studied samples, at 1 kHz.

Figure 1. SEM micrographs show the microstructure of CaCu3Ti 4O12 sintered ceramics prepared at 1060 °C for 5 h, where (a) and (b) are at two different magnifications.
Figure 2. Complex impedance plane plots of CaCu3Ti4O12 ceramics measured at RT – 200 °C; (a) and (b) show the impedance from RT to 100 °C and from 125 °C to 200 °C respectively, (c) is the high frequency data, and (d) is the impedence data measured at 200 °C.
Figure 3. Frequency dispersion of (a) real part of the dielectric constant and (b) loss tangent in the frequency range from 1 Hz to 3.5 MHz.

Figure 1: XRD pattern of A_xSr_2-xTiFeO₆ (A= Ba, Ca, La) with x=0.1
Figure 2: SEM images showing microstructure of (a) BSTF, (b) CSTF and (c) LSTF for x=0.2 composition.
Figure 3: Comparison of electrical conductivity, Seebeck coefficient and power factor of STF with BSTF, CSTF, and LSTF with compositions x=0.1 (Top Row), 0.2 (Middle Row) and 0.3 (Bottom Row) respectively.

Figure 1 Reactor for continuous pig iron making in 12.5 kW microwave furnace and a view of pig iron droplets
Figure 2 Microwave furnace with 20kW, radiating 8 microwave beams into the center of load chamber through hilical anntenas
Figure 3 Reactor of continuous production of pig iron by microwave heating
Figure 4 Change of temperature in reactor, oxygen partial pressure in out gas, forward and reverse microwave powers and microwave generating rate (MWGR)
Figure 5 Load chamber and reactor in 120kW microwave furnace
Figure 6 Pig iron poured out from the bottom of crucible in 120kW microwave furnace
Figure 7 Required energy for heating and reaction to make iron as a function of n
Figure 8 Reaction path of magnetite ore with graphite to produce iron on the phase diagram of Fe-O-C system. The reaction path is calculated from the oxygen potential in Figure 4.
Figure 9 Effect of microwave on reaction kinetic

Figure 1. Basics of laser peening process (Ref.: website of Curtiss-wright surface technologies)
Figure 2. AISI L6 tool steel specimen after laser peening
Figure 3. Test specimen and pin on disk tribometer used in wear testing
Figure 4. SEM image of cut section of laser peened surface
Figure 5. Residual stress distribution from surface layers
Figure 6. Hardness distribution along with surface layers
Figure 7. Wear rate for laser peening sample
Figure 8. coefficient of friction for different laser peening sample

Figure 1. A schematic showing the free energy path of a thermally-activated process under pure-ly thermal conditions. The forward reaction proceeds in time from the initial-reactant state to the final-product state driven by DF = -ΔG°.
Figure 2. Free energy path of a thermodynamically feasible process in a “wave-field-homogeneous” system under CPR MWI. The process under purely thermal conditions is also shown in dotted lines () for reference. F G° < 0, Æ^§ < Æ°.
Figure 3. DF-induced vacancy concentration gradients and vacancy flows during sintering: (a) under conventional isothermal conditions, (b) under isothermal and local non-uniform wave-field conditions.
Figure 4. A schematic showing the thermodynamics of a 1^st-order (phase) transformation at con-stant composition with and without the influence of a uniform resonant MW-field. -phase is assumed to be highly polarizable, whereas β-phase is non-polarizable under CPR MWI. For il-lustrative clarity, curvatures of the free-energy-level lines for α°, α^EM, and β°/β^EM are not shown.

Figure 1. As-received overhead window with white arrows depicting locations of carrier panel tiles and black arrows show the thermal pane glass fragments. One carrier panel was previously removed from the window frame.
Figure 2. Forward starboard carrier panel tile (a) with evidence of tile slumping and exposed silica fibers. Forward port side tile (b) with discolorations.
Figure 3. Images a and b show areas with yellow and blue discolorations on the aft TPS surface of two carrier panel tiles. Images c and d correspond to carrier panel in b and show indications of metallic deposits.
Figure 4. Micrographs of the unaffected tile specimen at the surface (a) and cross-section (b).
Figure 5. SEM cross-sections of carrier panel tile specimens sample 1 (a and b) and sample 2 (c and d). The TPS coating is illustrated on 4a and a lighter grey area was present on 4b. The coating in 4c had porosity and cracks. Micrograph 4c indicated other white phases present at the top edge of the specimen as pointed out by the black arrows.
Figure 6. EDS results of the unaffected sample at the surface (a) and at the coating of the cross-section (b).
Figure 7. EDS measurements of anomalous surface features shown. A selected spot for sample 1 is shown in (a) while (b) depicts a spot located on the sample 2 surface.
Figure 8. EDS spot measurements the metallic deposits (a and b) in sample 2 primarily consisting of Al.
Figure 9. Diffraction pattern of Sample 1 at the anomalous discoloration of the surface shown.
Figure 10. XRD pattern of a metallic striped area of sample 2.
Figure 11. XRD pattern measured at blue and yellow deposits of sample 2.
Figure 12. Selected spot measurements for EDS analysis as shown in a-c from sample 1 cross-section.
Figure 13. X–rayra maps of the scanned area in 8a (sample 2)and the resulting EDS spectra.

Figure 1. CMC Fabrication via the PIP Process
Figure 2. CMC Radial Bearings for Industrial Pump Applications
Figure 3. CMC Rocket and Small Arms Components

Figure 1: a) carbon fiber preform b) as-manufactured block of ZURAM.
Figure 2: Force-displacement graphs of the compression tests.
Figure 3: Transverse strain of sample Z#8 at progressing times.
Figure 4: Longitudinal, transverse strain and derived poisson numbers for samples Z#7 and Z#8.
Figure 5: Load over displacement from compression testing with fibers in load direction.
Figure 6: Setup of the shear tests.
Figure 7: Typical fracture pattern of the shear specimens (Z#75).
Figure 8: Load – displacement graphs of the shear tests.
Figure 9: a) Shape of the tensile samples b) sample with dot pattern c) sample under load d) sample after fracture
Figure 10: Force-displacement graphs of the tensile tests.
Figure 11: Stress distribution in the sample.
Figure 12: Determination of the local failure strain.
Figure 13: Determination of the poisson numbers in the tensile tests.
Figure 14: Tensile sample for testing normal to fibers.

Figure 1: Bright field TEM micrographs captured from individual still frames. A shows the initial state and B shows the microstructure after 35s of exposure. Pits present before exposure are circled in both A and B. The arrow in B highlights a thin segment of material separating two distinct corrosion events. The squared region is explored in further detail in Fig. 2.
Figure 2: A time lapse series of micrographs detailing one corrosion event. Each image represent one frame from a video recorded at 13.75 frames per second. The evidence of dissolution can be seen by the change of contrast beginning in B that gradually spread through grains surrounding the sample. The dark grain in the center, indicated by an arrow in C, appears to be more resistant to corrosion.
Figure 3: Growth of a large scale dissolution event. The circle in A highlights the initiation of a corrosion event and the arrow in D shows an example of non-curvature driven growth.
Figure 4. Corrosion front moving through the iron thin film. A, B, and C show the same location but separated by several seconds. Horizontal frames are separated by 0.01 s each. Corrosion initiation events are indicated by arrows.
Figure 5: Dissolution of grains surrounding an abnormally large grain. A shows the initial observation of the area, and B-F demonstrate how the material surrounding the abnormal grain is dissolved leaving it isolated. A small protrusion from the abnormal grain is highlighted by an arrow in A.

Figure 1. Effect of pH on removal and reduction of chromium(VI) from the potassium bichromate(VI) solution using persimmon gel.
Figure 2. Effect of pH on removal and reduction of chromium (VI) from the potassium bichromate (VI) solution using A. nicotianae cells.
Figure 3. Effect of pH on the removal of chromium from a chromium(III) nitrate solution using persimmon gel.
Figure 4. Effect of pH on the removal of chromium from a chromium(III) nitrate solution using A. nicotianae cells.
Figure 5. Effect of temperature on the desorption of chromium from chromium(VI) adsorbed using persimmon gel in 1 M hydrochloric acid.
Figure 6. Time course of the removal of chromium from the potassium bichromate (VI) solution by the persimmon tannin adsorbent.
Figure 7. Effect of temperature on chromium(III) desorption from chromium(III) adsorbed using A. nicotianae cells in diluted hydorochloric acid.
Figure 8. Effect of cell amount on each metal removal from the chromium (VI) plating wastewater sample I using A. nicotianae cell
Figure 9. Effect of persimmon gel amount on the removal of each metal from chromium(VI) plating wastewater with partially removed metals using persimmon gel.
Figure 10. Desorption of adsorbed metals from chromium(VI) plating wastewater with diluted hydrochloric acid at reflux temperature.

Figure 1. SEM images of (a) Ti6Al4Valloy, (b) TiNi, (c) TiNi5ZrO2 and (d) TiNi10ZrO2 laser cladded composites.
Figure 2. Microhardness of substrate and coated samples
Figure 3. Overall open circuit potential versus time before, during and after sliding test in 3.5 % NaCl solution.
Figure 4. Coefficient of friction under open circuit potential for all specimens in 3.5 % NaCl solution.
Figure 5. Potentiodynamic polarisation curves of Ti6Al4V substrate and coated samples in 3.5% NaCl solution.
Figure 6. Corrosion current densities of Ti6Al4V substrate and coatings in 3.5% NaCl.
Figure 7. Potentiodynamic polarization curves of Ti6Al4V and coated samples under sliding load of 5 N in 3.5 % NaCl.
Figure 8. Tribocorrosion current densities of Ti6Al4V substrate and coatings in 3.5% NaCl.

Figure 1. Raman spectra of the solid solution crystals ZrO₂-Y₂O₃.
Figure 2. TEM images - (a) 2.5YSZ; (b) 3.7YSZ; (c) 6YSZ; (d) 8YSZ. The insets show diffraction patterns of the respective crystal regions.
Figure 3. The dependences of conductivity of (2.5-15)YSZ on the inverse temperature in the Arrhenius coordinates (a); Conductivity and activation energy as functions of Y₂O₃ concentration (b).
Figure 4. Raman spectra of the (ZrO₂)1-x(Sc₂O₃)x crystals.
Figure 5. TEM images of the (ZrO₂)1-x(Sc₂O₃)x crystals: (a) 6ScSZ; (b) 9ScSZ; (c) 10ScSZ; (d) 11ScSZ. The insets show diffraction patterns of the respective crystal specimen regions.
Figure 6. Arrhenius plot of electrical conductivities for the samples: 6ScSZ, 9ScSZ, 10ScSZ, 11ScSZ and 8YSZ for comparison.
Figure 7. The dependences of conductivity for the (ZrO₂)1-x-y(Sc₂O₃)x(Y₂O₃)y crystals on the inverse temperature in the Arrhenius coordinates.

Figure 1. Surface morphology of the just-fabricated LA-MA/PMIA fibrous membranes prepared at different core feeding rates.
Figure 2. The variations of fiber diameter with different core feeding rates and subsequent ethanol treatment.
Figure 3. Surface morphology of the ethanol-treated fibrous membranes.
Figure 4. Cross section appearance of the ethanol-treated individual fibers and fibrous membranes.
Figure 5. CLSM images of the untreated individual composite fibers. (a) coumarin (green), (b) rhodamine B (red) and (c) the merger of coumarin and rhodamine B
Figure 6. TG curves of neat LA-MA powder and related fibrous membranes.

Figure 1: Representative side view of contact angle formed between equilibrium (stable liquids) and quasi-equilibrium (metastable states) sessile PEO droplets and silanol surface of silicon dioxide for (top row) (a) PEO-5, T=250 K, (b) PEO-5, T=273 K, (c) PEO-5, T=303 K and (bottom row) (d) PEO-30, T=250 K, (e) PEO-30, T = 300 K. The visualization software package VMD⁴⁰ was used to create all images presented in this work
Figure 2 – (a) 90 degree and (b) 20 degree impact event for PEO-5 at 273 K, liquid droplet travelling at 10 m/s. Time increases from left to right.
Figure 3 – Top-down view of final equilibrium droplet-substrate complex for a liquid PEO5 nanodroplet at 273K impacting the surface with net speed (a) 0 m/s, (b) 10 m/s, and (c) 100 m/s.
Figure 4 – 90 degree impact of metastable PEO30 at 250 K. Initial droplet velocity was 100 m/s. Time increase from top to bottom in each column and then from left to right.
Figure 5 – Sequence of events for a 20 degree impact event of metastable liquid droplet, PEO-30, T=250 K. Time increases from left to right.
Figure 6 – Final droplet-substrate equilibrium configurations obtained after the secondary impact of PEO5 liquid droplets and 273 K for (a) 90 degree direct impact, (b) 90 degree offset impact, and (c) 20 degree glancing angle direct impact.
Figure 7 – A 90 degree secondary direct impact event for PEO30 droplets at 250 K (metastable). Time increase from top to bottom in each column and then from left to right.
Figure 8 – Experimental measurement of the contact angle of a PEO-34 droplet at 373 K.

Figure 1. La-doped translucent zirconia ceramics (16 mm in diameter and 1mm in thickness).
Figure 2. Total forward transmission (sample thickness 1mm) of La-doped zirconia ceramics.
Figure 3. Scattered light profile of the transmitted light at D65 (sample thickness 1mm).
Figure 4. Rietveld analysis of the La-doped translucent zirconia ceramics.
Figure 5. High resolution EDS mapping of La-atom. Blue area represents cubic phase including La, while black areas is tetragonal phase.
Figure 6. Raman spectra of fractured surface and polished surface. Peak of monoclinic phase indicates as double circle.

Figure 1. Schematic of the spin -spray deposition process using a rotating heated platen and two aqueous spray solutions.
Figure 2. (a) Atomized liquid as it is spray onto the heated rotating platen and (b) the volume fraction of the micron-sized droplets covering the platen surface.
Figure 3. The micro-droplet regime (red) plotted showing to deposit higher quality films than the continuous liquid layer regime (black).
Figure 4. SEM images of Ni0.19Zn0.30Co0.05Fe2.46O4 (a) top-view and (b) column view.
Figure 5. Off-axis electron holography (a) electron gradient map and (b) Lorentz image with labeled magnetic domains and direction.

Preface

This volume contains 36 papers presented during the Materials Science & Technol-ogy 2016 Conference (MS&T’16), held October 23–27, 2016 at the Salt Palace Convention Center, Salt Lake City, Utah. Papers from the following symposia are included in this volume:

Advanced Materials for Harsh Environments
Advances in Dielectric Materials and Electronic Devices
Advances in Ceramic Matrix Composites
Ceramic Optical Materials
Controlled Synthesis, Processing, and Applications of Structural and Functional Nanomaterials
Innovative Processing and Synthesis of Ceramics, Glasses, and Composites
International Standards for Properties and Performance of Advanced Ceramics
Multifunctional Oxides
Rustum Roy Memorial Symposium on Processing and Performance of Materi-als Using Microwaves, Electric, and Magnetic Fields
Sintering and Related Powder Processing Science and Technology
Surface Properties of Biomaterials
Thermal Protection Materials and Systems
Zirconia Based Materials for Cutting Edge Technology

These conference symposia provided a forum for scientists, engineers, and tech-nologists to discuss and exchange state-of-the-art ideas, information, and technolo-gy on advanced methods and approaches for processing, synthesis, characteriza-tion, and applications of ceramics, glasses, and composites.

Each manuscript was peer-reviewed using The American Ceramic Society’s re-view process. The editors wish to extend their gratitude and appreciation to all the authors for their submissions and revisions of manuscripts, to all the participants and session chairs for their time and effort, and to all the reviewers for their valu-able comments and suggestions.

We hope that this volume will serve as a useful reference for the professionals working in the field of synthesis and processing of ceramics and composites as well as their properties.

NAROTTAM P. BANSAL

RICARDO H. R. CASTRO

MICHAEL JENKINS

AMIT BANDYOPADHYAY

SUSMITA BOSE

AMAR BHALLA

J.P. SINGH

MORSI M. MAHMOUD

GARY PICKRELL

SYLVIA JOHNSON