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ISBN: 978-1-119-32013-5
ISSN: 0196-6219

CONTENTS

Preface

Introduction

International Standards for Properties And Performance of Advanced Ceramics – 30 Years of Excellence

Abstract
Introduction and Background
Conclusions
Acknowledgement
References

Stable Fracture Testing of Brittle Materials

Abstract
Introduction
Experimental
Results and Discussion
Conclusions
AcknowledgementS
References

Adventures and Misadventures in Applying ASTM Standard Test Method C 1421 to Measurements of the Fracture Toughness, K_IC, of Glasses

Abstract
Introduction
Materials
Experimental Proceedure
Results
Discussion
Conclusions
AcknowledgementS
References
Notes

Effects of Aqueous Solutions on Slow Crack Growth of Soda Lime Silicate Glass

Abstract
Introduction
Symbols
Procedure
Data Analysis
Inert and Time-dependent Strength
Test Variance
Conclusions
References
Notes

Modified Asymmetric Four-Point Bend Test Method for In-Plane Shear Properties of Ceramic Matrix Composites at Elevated Temperatures

Abstract
1. Introduction
2. CONCEPT
3. Experiment
4. Result
5. Discussion
6. Conclusion
7. Acknowledgement
References

Development of Transthickness Tension Test Method for Ceramic Matrix Composites at Elevated Temperatures

Abstract
1. Introduction
2. Concept
3. Experiment
4. Results
5. Discussion
6. Conclusions
7. Acknowledgement
References

Fatigue Behavior of SIC/SIC Ceramic Matrix Composites

Abstract
1. Introduction
2. Experimental ProcedureS
3. Results and Discussion
Summary
AcknowledgementS
References

Tension-Compression Fatigue of a Nextel^™720/Alumina Composite at 1200° C in Air and in Steam

Abstract
Introduction
Material and Experimental Arrangements
Results and Discussion
Concluding Remarks
Acknowledgement
References
Notes

Facility for Testing SiC Fiber Tows at Elevated Temperature in Silicic Acid-Saturated Steam

Abstract
Introduction
Development and Main Features of the Test Facility
Concluding Remarks
Acknowledgement
References

Fiber Strength of Hi-Nicalon^™-S After Oxidation and Scale Crystallization in Si(OH)₄ Saturated Steam

Abstract
Introduction
ExperimentS
Results and Discussion
Summary and Conclusions
References

Long Term Durability Results From Ceramic Matrix Composites: Comparison Across Multiple Material Systems (Part I)

Abstract
Introduction
Procedure
Results
Discussion
Conclusion
Future Work
Acknowledgments
References

Influence of Curvature on High Velocity Impact of SIC/SIC Composites

Abstract
Introduction
Experimental Procedure
Results and Discussion
Conclusion
AcknowledgementS
References

Characterization of Deformation and Damage in Porous SOFC Components via Spherical Indentation and Simulation

Abstract
Introduction
Experimental
Results and Discussion
Conclusion
Acknowledgement
References

Micro-Scale Sand Particles within the Hot-Section of a Gas Turbine Engine

Abstract
Introduction
Methodology
Results and Discussion
Conclusions
AcknowledgementS
References

Sintering Properties of TiB₂ Synthesized from Carbon Coated Precursors

Abstract
Introduction
Experimental
Resutls and DiscussionS
Conclusion
Acknowledgement
Reference

Microstructure and Phase Relationship of Aluminum Boride/Carbide Composites

Abstract
Introduction
Test Methods and Sample Preparation
Results and Discussion
Summary
Acknowledgement
References

Application of FeNbC as a Hardfacing Material Using Laser Cladding – Part II

Abstract
Introduction
Wear in Mining and Minerals Processing
FENBC Laser Cladding Process for the Wheel Loader Bucket Teeth
Field Trials of the Loader Bucket Teeth
Conclusions
References

Pressurless Infiltration of Al₂O₃ Preform Containing Aligned Two-Dimensional Channels with Al-Mg-Si Alloy

Abstract
Introduction
Experimental
Results and Discussion
Continuing ExperimentS
Conclusions
Acknowledgments
References

Functional Properties of MWCNT-Alumina Composites Prepared by Novel Approach

Abstract
Introduction
Experimental
Results and Discussion
Conclusion
Acknowledgement
References

Strength Improvements in Clay-Based Ceramic Reinforced with Discontinuous Basalt Fiber

Abstract
Introduction
Experimental Methods
Results and Discussion
Conclusions
Future Work
AcknowledgementS
References

An Experimental Study on Fabrication, Mechanical Behavior Characterization and Micro Structural Evolution in Glass-Metal Joints

Abstract
Introduction
Result and Discussion
Conclusions
AcknowledgementS
References

A Multiscale Analysis Tool for Predicting Flat Coupon Analysis Based Behavior of Ceramic Matrix Composite Components/Sub-Elements

Summary
Introduction
Technical Approach
Numerical Analysis: Results and Discussion
Uniaxial Tensile Test
Conclusion
References

Simulation and Experimental Validation of the Deformation and Stress Evolution During Cosintering of Ceramic Laminated Composites

Abstract
Introduction
Establishment of the Co-sintering Model
Materials
FE Modeling
Results
Discussion
Conclusions
AcknowledgementS
References

Author Index

EULA

List of Tables

Chapter 2

Table I Room temperature toughness values reported for alumina
Table II Room temperature toughness values reported for mullite
Table III toughness parameters for alumina
Table IV toughness parameters for mullite

Chapter 3

Table 1 Glasses tested. Mass percents are from Ref. 15 or the manufacturer where available
Table 2 Inert dry-nitrogen plateau fracture toughness values

Chapter 4

Table I —REGRESSION STATISTICS AND SLOW CRACK GROWTH (SCG) PARAMETERS
Table II —COEFFICIENT OF VARIATION (CV) IN PERCENT FOR TEST SETS

Chapter 05

Table 1 Test configurations

Chapter 6

Table 1 Test configurations

Chapter 7

Table 1 Applied material system of this study
Table 2 Fatigue test conditions

Chapter 11

Table I Material Summary

Chapter 12

Table I Impact velocities and energies for each specimen
Table II Impact event energy and change in electrical resistance

Chapter 13

Table 1 Summary of specimen properties measured
Table 2 Other fitting parameters, including the Gurson yield stress

Chapter 14

Table 1 Relevant thermodynamic and mechanical properties of the AFRL 02/03 synthetic sand used in the phase behavior simulations

Chapter 15

Table 1 Comparison of synthesized TiB₂ sintering with 3 wt. % cobalt with previous research

Chapter 16

Table I Test Matrix for Al-B-C Experiments
Table II Qualitative Phase Analysis via X-Ray Diffraction

Chapter 18

Table I Infiltration trial information

Chapter 21

Table 1 Chemical composition of metal specimens
Table 2 Chemical composition of different glass used
Table 3 Shear strength of different glasses with Austenitic stainless steel and Copper
Table 4 Micro hardness at different operating conditions

Chapter 22

Table I Elastic properties of the dense matrix phase (Gowayed, Ojard, Prevost, U, & Jefferson, 2013) and defects phase at microscale
Table II Elastic properties of the mesoscale matrix phase
Table III Calibrated transverse-isotropic properties of tows at room temperature
Table IV Calibrated matrix anisotropic properties at room temperature
Table V Comparison between experimental and simulation elastic properties at room temperature
Table VI Calibrated CZM model parameters from Mode I DCB analyses

Chapter 23

Table I Material parameters used in the model for materials A and B
Table II Simulation results for free sintering of materials A and B in comparison with experimental data
Table III Simulated longitudinal (δ_l) and transverse (δ_t) deflection for constrained sintering of a bilayer ceramic in comparison with experimental data (see also Fig. 4)

List of Illustrations

Chapter 1

Figure 1 – Timeline for three decades of ASTM Committee C28
Figure 2 Membership of ASTM Committee C28 from 1986 to Present
Figure 3 Pctorial illustration of Committee C28 standards
Figure 4 – Cumulative number of Committee C28 standards and number of standard needing mandatory review in any given year

Chapter 2

Figure 1 Schematic representation of the Griffith locus of a SENB specimen of a brittle material tested in 3-point bending
Figure 2 Load-time curve recorded during stable testing o spinel. Curve b) is a detail of a)
Figure 3 Griffith locus for the testing geometry used and different brittleness values, s. α_c=critical relative notch
Figure 4 Griffith locus for the testing conditions used: geometry, system compliance and material properties. α_c=critical relative notch
Figure 5 Characteristic curves recorded for alumina tested using CMOD (1.8μm/min, 1) and displacement (0.005mm/min, 2) as control parameters. a) Load-time, b) Load-displacement
Figure 6 Characteristic curves recorded for mullite tested using CMOD (18μm/min, 1) and displacement (0 .0 5mm /min, 2 ) as control parameters. a) Load-time, b) Load-displacement

Chapter 3

Figure 1 Common fracture toughness test configurations for ceramics and glasses
Figure 2 The classic crack velocity versus stress intensity (K-V) diagram
Figure 3 Good precracks. (a) and (b) are borosilicate crown precracks. Slight irregularities along the tensile surface from the hand grinding are inconsequential. (b) shows stable crack extension since this test was done in air at a slow loading rate. (c) and (d) are the same borofloat specimen. (d) is tilted back to reveal the median crack is slightly bowed, which causes the twist hackle steps on the sides 1. (e) and (f) are soda lime silica precracks. The secondary chipping in the top half of (f) was inconsequential since it occurred after breakage. (g) and (h) show the same crack in a Starfire specimen. There is no clear boundary on the right side suggesting the crack went critical on that side. Notice the ground surface had no effect on the precracks in (d) and (h)
Figure 4 Rejected precracks. All are borosilicate crown, BK-7 pieces. (a) has a precrack with steps and irregularities because the median precrack actually dived beneath the exposed fracture surface on the right side. (b) shows a precrack with too many steps and irregularities. (c) shows what appear to be a perfect precrack, but the maximum Y for this shape is at the surface. Not enough material was ground away to shape the crack. (d) shows the opposite problem whereby too much was removed and a semi-ellipse is a poor approximation to the true shape
Figure 5 Results for borosilicate crown, BK-7 optical glass. The number of specimens and the average times to failure are shown for each data set
Figure 6 Results for (a), borosilicate “borofloat 1,” and (b), borosilicate 2 “borofloat 2.”
Figure 7 Results for (a), the soda lime silica (a), and (b) the Starfire version of soda lime silica
Figure 8 Unusual BK-7 borosilicate crown specimens. These were tested at the fastest rate in dry nitrogen. (a) and (b) are the same specimen. The computed K_Ic was 1.61 MPa√m. (c) was an unusually strong specimen with a computed K_Ic of 1.69 MPa√m. Notice the unusual mirror-to-flaw size ratios. These precracks behaved as though they had partially healed

Chapter 4

Figure 1 Siloxane dissolution by water, as described by Michalske and Freiman in Reference 2
Figure 2 — Water interaction with positive sodium film, attached to slightly susceptible siloxane bonds at glass flaw site
Figure 3 —Fracture stress as a function of stress rate for fits to mean and median values with 95 percent confidence interval
Figure 4 —Crack velocity as a function of stress intensity

Chapter 5

Fig. 1 Concept of AFPB
Fig. 2 Schematic of typical AFPB test
Fig. 3 Spacer for buffering
Fig. 4 IPS strength of room temperature Iosipescu (Iosipescu RT), Room temperature AFPB (AFPB RT) and High-temperature AFPB (AFPB HT)
Fig. 5 In-plane shear stress-displacement curves of Room temperature Iosipescu (Iosipescu RT), Room temperature AFPB (AFPB RT) and High-temperature AFPB (AFPB HT)
Fig. 6 Fracture surfaces of Room temperature Iosipescu (a), Room temperature AFPB (b) and High-temperature AFPB (c)
Fig. 7 DIC Results of Room temperature Iosipescu (a), Room temperature AFPB (b) and High-temperature AFPB (c) at in-plane shear stress 60 MPa
Fig. 8 FEM Result
Fig. 9 Shear stress distribution shown in Fig. 8

Chapter 6

Fig. 1-1 SGT specimen: rectangular
Fig. 1-2 SGT specimen: circular
Fig. 2 Schematic of SGT
Fig. 3 Concept of QNT. (a) Bird's-eye viewand three views of test specimen with applied load. (b) Bird’s-eye view of test setup
Fig. 4 Dimensions of Quadruple-Notched Test Specimen
Fig. 5 SGT specimen after fracture. Left; rectangular Right; circular
Fig. 6 QNT specimen after fracture
Fig. 7 Flatwise specimen after fracture
Fig. 8 Test results
Fig. 9 TT stress-Displacement curve
Fig. 10 SGT circular FEM result at arrow section
Fig. 11 QNT FEM result at arrow section

Chapter 7

Fig. 1 Dimensions of the tensile and fatigue test specimen (mm)
Fig. 2 Dimensions of the notched specimen (mm)
Fig. 3 Typical stress-strain curve of CMC
Fig. 4 Fatigue test results of smooth and notched specimens
Fig. 5 Strain distribution of the notched specimens at 60MPa by DIC (Room Temp.)
Fig. 6 Modulus change (1100C; smooth, 10mm gage width)
Fig. 7 Permanent strain (1100C; smooth, 10mm gage width)
Fig. 8 Cross section of test specimens (smooth) after the fatigue test

Chapter 8

Figure 1 As-received material: (a) overview, (b) porous nature of the matrix is evident
Figure 2 Test specimen for (a) tension-tension cyclic testing with R = 0.05, (b) tension-compression cyclic testing with R = -1.0. All dimensions in millimeters
Figure 3 Fatigue S-N curves for N720/A at 1200°C in air and in steam. Arrow indicates that failure of specimen did not occur when the test was terminated. Tension-tension fatigue data for R = 0.05 from Ruggles-Wrenn et al
Figure 4 Typical evolution of stress-strain hysteresis response of N720/A composite with fatigue cycles at 1200°C (a) in air and (b) in steam. σ_max = 90 MPa
Figure 5 Maximum and minimum strains vs. fatigue cycles at 1200°C in (a) in air, (b) in air and in steam
Figure 6 Normalized tensile modulus vs. fatigue cycles at 1200°C in (a) air, (b) air and steam
Figure 7 Retained tensile strength (a) and retained tensile modulus (b) of the N720/A specimens subjected to prior cyclic testing in laboratory air and in steam environment at 1200°C. Tension-tension fatigue data from Ruggles-Wrenn et al
Figure 8 Fracture surfaces of N720/A specimens tested in tension-compression cyclic fatigue at 1200°C: (a) in air, σ_max = 100 MPa, N_f = 5264 cycles, t_f = 1.5 h, (b) in steam, σ_max = 100 MPa, N_f = 450 cycles, t_f = 0.13 h, (c) in air, σ_max = 80 MPa, N_f = 113382 cycles, t_f = 31.5 h, and (d) in steam, σ_max = 75 MPa, N_f = 86548 cycles, t_f = 24 h
Figure 9 Fracture surfaces of N720/A specimen tested in tension-compression cyclic fatigue at 1200° C. Compression curl fiber fractures
Figure 10 Fracture surface of N720/A specimen tested in tension-compression cyclic fatigue at 1200° C. Fiber failure due to bending

Chapter 9

Figure 1 Basic setup for creep testing ceramic fiber tows at elevated temperature in air and in steam
Figure 2 Temperature profiles obtained in air. Data from Steffens and Shillig are included for comparison
Figure 3 Temperature profiles obtained in silicic acid-saturated steam in current work and data obtained in unsaturated steam from Steffens and Shillig
Figure 4 SEM micrographs of the Hi-Nicalon^™-S fiber tow subjected to creep at 800°C in steam. Variations along the length of the fiber tow are evident. (a) Fiber degradation due to active oxidation, typically found in bottom sections of the fiber tow. (b) SiO2 scale growth due to passive oxidation typically found in top sections of the fiber tow. Reproduced from Ref. 37
Figure 5 Layers of alumina block insulation and aluminosilicate blanket insulation assembled between the heating unit (right) and the test furnace (left)
Figure 6 Facility for creep testing ceramic fiber tows at elevated temperature in steam saturated with silicic acid
Figure 7 SEM micrographs of the Hi-Nicalon^™ S SiC fiber tow tested in creep at 2.96 MPa and 800°C in steam saturated with silicic acid. (a)-(b) Bottom of the specimen gage section. (c)-(d) Center of the gage section. (e)-(f) Top of the gage section
Figure 8 The EDS analysis of the light-colored layer on the surface of Hi-Nicalon^™ S SiC fibers tested in creep at 2.96 MPa and 800°C in steam saturated with silicic acid shows a decrease in carbon and an increase in silicon and oxygen content. Approximate composition of the light-colored surface layer: 73 at.% Si, 16 at.% C, and 10 at.% O
Figure 9 The EDS analysis of the dark-hued areas on the surface of Hi-Nicalon^™ S SiC fibers tested in creep at 2.96 MPa and 800°C in steam saturated with silicic acid shows low oxygen content (7 at,% O) and a near-stoichiometric SiC composition (46.5 at.% S, 45 at.% C)
Figure 10 The EDS analysis of the interior of Hi-Nicalon^™ S SiC fibers tested in creep at 2.96 MPa and 800°C in steam saturated with silicic acid shows negligible oxygen content (1.5 at.% O) and a near-stoichiometric SiC composition (49 at.% S, 49 at.% C)

Chapter 10

Figure 1 Schematic diagram of equipment used to oxidize SiC fibers in Si(OH)₄ saturated steam
Figure 2 Average fiber tensile strength (σ_av) of Hi-Nicalon^™-S after heat-treatment in Si(OH))₄
Figure 3 Optical transmitted light micrographs of SiO₂ scale dewetting after oxidation in steam at 700° and 800°C. Some scales formed at 800°C were facetted and crystallized to cristobalite
Figure 4 Log-log plot of SiO₂ scale thickness on Hi-Nicalon^™ -S formed after oxidation in Si(OH)₄ saturated steam
Figure 5 Optical transmitted light micrographs of SiO₂ scales formed on Hi Nicalon ^™ -S after oxidation in Si(OH)₄ saturated steam at 1300°C for 30 h and 1400°C for 10 h
Figure 6 TEM micrograph of scale formed in 1 h on Hi-Nicalon^™-S in Si(OH)4 saturated steam at 1000°C. SAID insets, from left to right, show: Ring pattern for β-SiC; Ring pattern for α-cristobalite; Ring pattern for α-cristobalite superimposed on a single crystal α-cristobalite pattern, and; [001] Single-crystal pattern for α-cristobalite
Figure 7 TEM micrograph of scale formed in 3 h on Hi-Nicalon^™-S in Si(OH)₄ saturated steam at 1000°C
Figure 8 TEM micrograph of scale formed in 1 h on Hi-Nicalon^™-S in Si(OH)₄ saturated steam at 1200°C
Figure 9 TEM micrographs of scale formed in 3 h on Hi-Nicalon^™-S in Si(OH)₄ saturated steam at 1400°C. a) Coarse-grained cristobalite scale. b) SiO₂ glass scale. c) Very coarse-grained cristobalite scale
Figure 10 TEM micrographs of scale formed in 1 and 3 h on Hi-Nicalon^™-S in Si(OH)₄ saturated steam at 1500°C. a) Very coarse-grained cristobalite scale formed after 3h at 1500°C. b) Relatively fine-grained cristobalite scale formed after 3h at 1500°C. c) Very coarse-grained cristobalite scale formed after 1h at 1500°C. d) Relatively fine columnar-grained cristobalite scale formed after 1h at 1500°C
Figure 11 TEM micrographs of Hi-Nicalon^™-S SiC fiber microstructure after 3 h oxidation in Si(OH)₄ saturated steam at 1500°C. a) Low magnification image of the SiO₂ - SiC interface. b) Intermediate magnification of the SiC fiber. c) High resolution image of the SiC fiber, showing SiC grains and facetted SiOC inclusions with turbostratic graphite d) An even higher magnification image of the area in “c” showing an SiOC glass pocket with turbostratic graphite

Chapter 11

Figure 1 Creep Results on Testing of S200
Figure 2 Creep Results on Testing of MI SiC/SiC
Figure 3 Creep Results on Testing of A410
Figure 4 Creep Results for all 4 CMC systems at the highest test temperatures (for that CMC System)
Figure 5 Creep Results for all 4 CMC systems at the lowest test temperatures (for that CMC System)
Figure 6 High Temperature Creep Results (Figure 4) with Fitted Curves (fit lines extrapolated to shorter and longer times)
Figure 7 CMC and Metal Creep Rupture Data

Chapter 12

Figure I Dimensions of c-coupon specimens with (A) 12.7 mm width and (B) 5.6 mm width
Figure II Schematic of specimen support fixtures for (A) c-coupon and (B) c-coupon arms
Figure III Absolute change in electrical resistance as a function of the absorbed energy by the system. (All dimensions are in mm)
Figure IV Micro-CT images of 12.7 mm c-coupon that show (A) scanned volume of the impact site, (B) a cross-section view sliced at the center of the impact damage and (C) scanned volume of the back side. Circles indicate select regions of porosity
Figure V Micro-CT images of 12.7 mm arm that show (A) the scanned volume of the impact site and (B) a side-view of the back side damage
Figure VI Micro-CT images of 5.6 mm c-coupon showing (A) the scanned volume of the impact site, (B) a cross-section view and (C) the scanned volume of the back side
Figure VII Micro-CT images of 5.6 mm arm that demonstrate (A) the scanned volume of the impact site and (B) a cross-sectional view sliced at the center of the impact site and back side damage
Figure VIII Cross-sections of 12.7 mm specimens that illustrate the difference between (A) the impact site of the curved portion of the c-coupon and (B) the impact region of the c-coupon arm
Figure IX Cross-sections of 5.6 mm specimens showing (A) the impact damage of the curved portion of the c-coupon compared to (B) the impact morphology of the c-coupon arm

Chapter 13

Fig. 1 Schematics of the 2D FEM simulation of spherical indentation of (a) a porous bulk LSCF and (b) a porous LSCF thin layer on a dense substrate
Fig. 2 Loading-unloading curves generated from experiments and best fit FEM simulation curves for samples sintered at temperatures of (a) 900 °C, (b) 1000°C, (c) 1100°C and (d) 1200°C
Fig. 3 Experimental and simulated E for samples sintered at (a-d) 900-1200 °C
Fig. 4 Experimental and simulated H_n for samples sintered at (a-d) 900-1200 °C
Fig. 5 (a) FIB-milled cross-section image. Densification zone indicated by dashed curves. (b) Contour plots of porosity distribution. (c-d) Close views of deformed and un-deformed zones. Arrows mark collapse of particles. (e) Porosity after indentation experiments and simulations. Bulk LSCF: Plastic Deformation
Fig. 6 Effect of the Gurson model in the FEM on the extraction of (a) Young’s modulus and (b) uniaxial yield stress. Results are normalised with data from standard models
Fig. 7 Experimental indentation load-depth curves generated at 1000 mN load (beyond each corresponding threshold load) for LSCF bulk specimens sintered at 900 °C and 1000 °C
Fig. 8 Radial cracks in the specimens after indentation (arrows show cracks): (a) Sintering T=900 °C, P=2800 mN, (b) Sintering T=1000 °C, P=3600 mN, (c) Sintering T=1100 °C, P=2400 mN, (d) Sintering T=1200 °C, P=6000 mN. (e) Cross-section outside contact circle of specimen in (a), showing no ring-cone cracks but a radial crack penetrating downward, (f) magnified view of a 1200 °C-specimen surface after 5000 mN indentation showing no ring cracks
Fig. 9 Contour plots of S₃₃ (in GPa) in an indentation cycle to 1200 mN, (a) loaded to 600 mN, (b) fully loaded at 1200 mN, (c) unloaded back to 600 mN, (d) fully unloaded. Compressive stress shown negative. Here, all the regions of compressive stress are shown in grey for clarity
Fig. 10 Residual stress effect on simulated loading-unloading curves compared to experimental curve for a LSCF film sintered at 1000 °C with 39.7% porosity and 10 μm thickness
Fig. 11 Porosity distribution after simulation for the film with (a) residual stress=0, (b) residual stress=100MPa, and (c) residual stress=300MPa and (d) the variation of residual porosity along the central line under the indenter with different residual stress incorporated (0 – 300MPa)
Fig. 12 Apparent E and H_n derived from the simulations as a function of residual stress in the film (negative values are compressive stresses)
Fig. 13 Effect of film thickness, at constant h_max of 1.97⊠m, on (a) indentation curves, (b) porosity distribution and (c) apparent E and H_n of the films
Fig. 14 Simulation results of apparent E and Hn as a function of h_max/t_f, by either fixing the depth and varying the thickness, or fixing the thickness and varying the depth
Fig. 15 Comparison between experimentally measured apparent E and H_n and values extracted from FEM simulations, as a function of h_max/t_f for the actual LSCF films sintered at 1000 °C
Fig. 16 Influence of densification on the apparent E and H_n for the base case

Chapter 14

Figure 1 This drawing shows the typical gas turbine engine used on U.S. military rotorcraft. The boxed section indicates the hot-section components: combustor, the gas generator turbines, and the power turbines
Figure 2 (a) Blades and (b) vanes with typical sand damage
Figure 3 A diagram of a typical coating system [reprinted with permission from AAAS]
Figure 4 The 2D axisymmetric geometry of a spherical sand particle. The inset shows the generated 3D geometry of the spherical sand particle
Figure 5 Core temperature of the larger (100⊠m → 500⊠m diameter) spherical sand particles as a function of time
Figure 6 Core temperature of the medium-sized (20⊠m → 100⊠m) spherical sand particles as a function of time. It is interesting to note the lack of a discontinuity for particles < 30⊠m
Figure 7 The computed melting times for particles of various sizes

Chapter 15

Fig 1 TEM micrographs of carbon coated precursors mixed with B₄C. (a) Overview of the mixtures, (b) enlarge view of carbon coated TiO₂
Fig 2 Weight loss of samples reacted at different temperature
Fig 3 XRD patterns for samples from carbon coated precursors mixed with B4C at different temperature. (a) 1100°C, (b) 1200°C, (c) 1300°C, (d) 1400°C, (e) 1500°C
Fig 4 Morphology of produced TiB₂ powders from 1500°C
Fig 5 Sintered density and percent of TD of produced TiB₂ sintering with different Co content
Fig 6 SEM and BSE micrographs of polished samples with different Co content. (a) SEM of sample with 3 wt. % Co, (b) BSE of sample with 3 wt. % Co, (c) SEM of sample with 10 wt. % Co, (d) SEM of sample with 20 wt. % Co
Fig 7 Mechanical properties of sintered samples with the change of Co content
Fig 8 Comparison of theoretical elastics modulus and measured value

Chapter 16

Figure 1 Diffraction pattern for the Aluminum alloy and Boron powder (Al-B) sample [Notice that the AlB₁₂ peaks are labeled (#4) on the plot]
Figure 2 SEM back-scattered image of sample Al-B highlighting the different phases present
Figure 3 Diffraction pattern for the Aluminum alloy, Boron & B₄C powder (Al-B-B₄C) sample [Notice that the AlB12 peaks are labeled (#4) on the plot]
Figure 4 SEM back-scattered image of sample Al-B-B₄C highlighting the different phases present
Figure 5 Diffraction pattern for the Aluminum alloy, Boron & Diamond powder (Al-B-D) sample
Figure 6 (A) SEM back-scattered image and color coded mapping images: (B) Boron locations (C) Al locations and (D) composite image of elements detected
Figure 7 50% Si – 50% Al alloy with Boron powder (5050-B) sample (a) diffraction pattern and (b) microstructure of sectioned surface
Figure 8 50% Si – 50% Al alloy with Boron powder and B₄C powder (5050-B-B₄C) sample (a) diffraction pattern and (b) microstructure of sectioned surface
Figure 9 Back-scattered image and a composite color coded mapping image highlighting the B, C, Al and Si locations for the 50% Si – 50% Al alloy with Boron and Diamond powder
Figure 10 70% Si – 30% Al alloy with (a) Boron powder, (b) Boron and B₄C powder, and (c) Boron and Diamond powder
Figure 11 Composite color coded mapping image of the 70%Si-30%Al Boron and Diamond sample highlighting the B, C, Al and Si locations

Chapter 17

Figure 1 Typical microstructure of FeNbC observed using optical microscopy with differential interference contrast (DIC) (a) and mapping of niobium by SEM/EDS (b). The NbC particle sizes are between 5 to 30μm
Figure 2 Appearance of different granules of FeNbC: <1 mm and 1-6 mm (a) and 6-12 mm and 12-25 mm (b)
Figure 3 Views of the Volvo wheel loader (a) and bucket teeth (b) at CBMM’s mine. The wheel loader bucket operates regularly with eight teeth or tips of low alloy carbon steel weighing approximately 11 kg each. The average service life of these conventional bucket teeth is 1,220 hours with best performance reaching approximately 1,340 hours
Figure 4 Coherent High Light 8000D laser system (a) and FeNbC laser cladding (b)
Figure 5 Volvo wheel loader steel teeth before (a) and after (b, c and d) coating with FeNbC
Figure 6 Macro (a) and microstructural (b, c and d) aspects of the interface between the carbon steel tip and the FeNbC layer deposited by laser cladding
Figure 7 Assembling of the loader bucket teeth. The four low alloy carbon steel tips coated with FeNbC (1, 2, 3 and 4) are indicated with arrows
Figure 8 Weight loss of the coated and uncoated teeth during the field trial
Figure 9 Wear patterns of the coated and uncoated teeth after the fifth inspection of the field trial (1,460h). Top (a) and bottom (b) views
Figure 10 Wear patterns of the coated teeth after the final inspection of the field trial (2,630h). Top (a) and bottom (b) views
Figure 11 Microstructural views of the worn teeth after the field trial
Figure 12 Morphology of the wear tracks at 22 °C after dry sliding tests of Fe₃Al-NbC (counter body: 99.7% alumina; s = 5,000 m (or 50,000 cycles), P_0max= ~660 MPa). (a) v = 1 m/s and (b) v = 7 m/s. [9]

Chapter 18

Figure 1 An example set-up for pressureless infiltration
Figure 2 Micrographs of the cross-section of composite sample with (a) complete or nearly complete infiltration (b) partial infiltration and (c) no infiltration
Figure 3 Micrographs of the cross-section of composite sample containing channels infiltrated with aluminum alloy. (a) Cracks propagate from the channel wall and (b) a clear interfacial area can be seen between ceramic and metal
Figure 4 Image of ceramic sample containing channels filled with metal in two directions

Chapter 19

Figure 1 Schematic of sintering regime for (a) hot pressing and (b) rapid hot pressing
Figure 2 SEM images of granulated alumina-CNT composite powder with 10 vol% of MWCNTs (a) with a detail of the distribution of MWCNTs on the surface of granules (b) and inside the granules (c)
Figure 3 Comparison of relative densities of Al₂O₃-MWCNTs composites sintered by HP and RHP
Figure 4 Fracture surfaces of the alumina-based composites with same 7.5 vol% content of MWCNTs: (a, b) prepared by rapid hot pressing and (c, d) prepared by hot pressing
Figure 5 Grain size of Al₂O₃-MWCNTs composites prepared by hot pressing (HP) and rapid hot pressing (RHP)
Figure 6 Raman spectra of raw MWCNT, functionalized MWCNTs and alumina-MWCNTs composites sintered by hot pressing and rapid hot pressing
Figure 7 Comparison of the temperature dependence of thermal diffusivity of composites sintered by (a) hot pressing and (b) rapid hot pressing
Figure 8 Comparison of the temperature dependence of the thermal conductivity of composites sintered by (a) hot pressing and (b) rapid hot pressing
Figure 9 Comparison of the electrical conductivity of Al₂O₃-based composites sintered by hot pressing and rapid hot pressing

Chapter 20

Figure 1 Three-point flexural strength of the unreinforced matrix ceramic at each tested firing temperature
Figure 2 Three-point flexural strength of samples reinforced with 20 wt% of milled basalt fiber at each firing temperature. Unreinforced matrix strengths are shown for comparison
Figure 3 Three-point flexural strengths of samples fired at 1050 °C with varying concentrations of milled basalt fiber
Figure 4 EDS element maps of a representative area on a polished cross-section of a sample fired at 1050 °C. For scale, scanned area shown is 160 μm wide by 120 μm high
Figure 5 EDS element maps of a representative area on a polished cross-section of a sample fired at 1150 °C. For scale, scanned area shown is 160 μm wide by 120 μm high

Chapter 21

Figure 1 Dimension of metal substrate and glass pallet
Figure 2 Glass pre-formation process
Figure 3 Lap joint for glass metal bond strength
Figure 4 X-Rays diffraction pattern of Authentic Stainless Steel at different operating conditions
Figure 5 X-Rays diffraction pattern of copper at different operating conditions
Figure 6, 7 Microstructure of Austenitic Stainless steel and Copper fresh Specimen at 100 μm
Figure 8, 9 Microstructure of Austenitic Stainless steel and Copper fresh Specimen at 100 μm
Figure 10, 11 Microstructure of Austenitic Stainless steel and Copper fresh Specimen at 100 μm

Chapter 22

Figure 1 Illustration of the spatial length scales include in the multiscale framework
Figure 2 Illustration of the multiscale framework prediction scheme
Figure 3 Micrographic image of 5HS MI SiC/SiC CMC (Gowayed, et al., 2007)
Figure 4 Schematic of the RVE analyses
Figure 5 Illustration of the mesoscale matrix resolved into dense matrix phase and the defects phase at the microscale
Figure 6 5HS MI SiC/SiC mesoscale RVE with tow phase and the matrix phase
Figure 7 Comparison between homogenized and experimental elastic properties
Figure 8 Schematic of the multiscale uniaxial tensile test along with symmetric FE model
Figure 9 Comparison between experimental and simulation uniaxial tensile test stress-strain data
Figure 10 Schematic and FE model of Mode-I DCB specimen and test configuration
Figure 11 Deformation of cohesive springs resolved to directions normal (Δn) and tangential (Δ_t) to the slave surfaces
Figure 12 Mode I traction-separation based cohesive behavior in normal direction
Figure 13 Mode-I DCB specimen with ‘CSDMG’ contours
Figure 14 Comparison between Mode I Force versus COD plots from simulation and experiments (Choi, 2008)
Figure 15 Comparison between Mode-I fracture toughness values from simulation and experiments (Choi, 2008)
Figure 16 Setup of model for ENF calibration
Figure 17 Mode II traction-separation based cohesive behavior in tangential direction
Figure 18 Mode-II ENF specimen (a) CSDMG line plot at crack-tip (b) contour plot of CSDMG
Figure 19 Comparison between Mode-I fracture toughness values from simulation and experiments (Choi, 2008)
Figure 20 Schematic and 3D FE model of C-channel specimen and test configuration
Figure 21 Comparison between experimental images and simulation contour plots of ‘CSDMG’ along load path
Figure 22 Comparison between simulation and experimental (Greg Ojard-UTRC) Force Vs Opening Displacement plots for MI SiC-SiC system

Chapter 23

Figure 1 Schematic of multilayer ceramic under co-sintering conditions
Figure 2 Longitudinal shrinkage of a 50 mm long Al₂O₃ sample with G_eq = 5 μm
Figure 3 Boundary conditions and shrinkage directions in the FEM model(l); Temperature profile for sintering (r)
Figure 4 Max. abs. principal stress and deflection (longitudinal (δ_l) and transversal (δ_t)) of a bilayer ceramic (Top layer material A, bottom layer material B) at room temperature after constrained sintering (l); Photograph of bilayer laminate after sintering (r)

Preface

This volume is a compilation of papers presented in the Mechanical Behavior and Performance of Ceramics & Composites symposium during the 40th International Conference & Exposition on Advanced Ceramics and Composites (ICACC) held January 24–29, 2016, in Daytona Beach, Florida.

This long-standing symposium received presentations on a wide variety of topics thus providing the opportunity for researchers in different areas of related fields to interact. This volume emphasizes some practical aspects of real-world engineering applications of materials such as oxidation, fatigue, fracture, impact, and mechani-cal behavior as associated with systems ranging from glasses to metal and ceramic-matrix composites to borides and carbides to sand. Symposium topics included:

Fabrication, Microstructure and Properties
Fatigue and Durability
Oxidation and Wear
Impact

Significant time and effort is required to organize a symposium and publish a proceeding volume. We would like to extend our sincere thanks and appreciation to the symposium organizers, invited speakers, session chairs, presenters, manuscript reviewers, and conference attendees for their enthusiastic participation and contri-butions. Finally, credit also goes to the dedicated, tireless and courteous staff at The American Ceramic Society for making this symposium a huge success.

JONATHAN SALEM
NASA Glenn Research Center

DILEEP SINGH
Argonne National Laboratory

Introduction

This collected proceedings consists of 104 papers that were submitted and approved for the proceedings of the 40th International Conference on Advanced Ceramics and Composites (ICACC), held January 24–29, 2016 in Daytona Beach, Florida. ICACC is the most prominent international meeting in the area of advanced struc-tural, 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. This year's meeting continued the tradition and added a few grand cele-brations to mark its 40th year.

The 40th ICACC hosted more than 1,100 attendees from 42 countries that gave over 900 presentations. The topics ranged from ceramic nanomaterials to structural reliability of ceramic components, which demonstrated the linkage between materi-als science developments at the atomic level and macro level structural applica-tions. Papers addressed material, model, and component development and investi-gated the interrelations between the processing, properties, and microstructure of ceramic materials.

Symposium 1	Mechanical Behavior and Performance of Ceramics and Composites
Symposium 2	Advanced Ceramic Coatings for Structural, Environmental, and Functional Applications
Symposium 3	13th 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 Direct Thermal Energy Conversion and Rechargeable Energy Storage
Symposium 7	10th International Symposium on Nanostructured Materials: Functional Nanomaterials and Thin Films for Sustainable Energy Harvesting, Environmental and Health Applications
Symposium 8	10th International Symposium on Advanced Processing & Manufacturing Technologies for Structural & Multifunctional Materials and Systems
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 Production Root Technology
Symposium 12	Materials for Extreme Environments: Ultrahigh Temperature Ceramics (UHTCs) and Nano-laminated Ternary Carbides and Nitrides (MAX Phases)
Symposium 13	Advanced Materials for Sustainable Nuclear Fission and Fusion Energy
Symposium 14	Crystalline Materials for Electrical, Optical and Medical Applications
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	Field Assisted Sintering and Related Phenomena at High Temperatures
Focused Session 6	Hybrid Materials and Processing Technologies
Special Symposium	40th Jubilee Symposium: Engineered Ceramics—Current Status and Future Prospects
Special Symposium	5th Global Young Investigators Forum
Special Symposium	Emerging Technologies Symposium: Carbon Nanostructures and 2D Materials and Composites

The proceedings papers from this conference are published in the below seven issues of the 2016 CESP; Volume 37, Issues 2–7, as listed below.

Mechanical Properties and Performance of Engineering Ceramics and Composites XI, CESP Volume 37, Issue 2 (includes papers from Symposium 1)
Advances in Solid Oxide Fuel Cells and Electronic Ceramics II, CESP Volume 37, Issue 3 (includes papers from Symposia 3 and 14)
Advances in Ceramic Armor, Bioceramics, and Porous Materials, CESP Volume 37, Issue 4 (includes papers from Symposia 4, 5, and 9)
Advanced Processing and Manufacturing Technologies for Nanostructured and Multifunctional Materials III, CESP Volume 37, Issue 5 (includes papers from Symposia 8 and 11 and Focused Sessions 4 and 5)
Ceramic Materials for Energy Applications VI, CESP Volume 37, Issue 6 (includes papers from Symposia 6 and 13 and Focused Session 2)
Developments in Strategic Materials II, CESP Volume 37, Issue 7 (includes papers from Symposia 2, 10, 12, Focused Sessions 1, and the Special Symposia on Carbon).

The organization of the Daytona Beach meeting and the publication of these pro-ceedings 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 atten-dees, for their efforts and enthusiastic participation in the vibrant and cutting-edge conference.

ACerS and the ECD invite you to attend the 41st International Conference on Advanced Ceramics and Composites (http://www.ceramics.org/icacc2017) January 23-28, 2017 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.

MANABU FUKUSHIMA, National Institute of Advanced Industrial Science and Technology (AIST), Japan

ANDREW GYEKENYESI, Ohio Aerospace Institute/NASA Glenn Research Center, USA

Volume Editors
August 2016

A Collection of Papers Presented at the 40th International Conference onAdvanced Ceramics and Composites January 24–29, 2016Daytona Beach, Florida

A Collection of Papers Presented at
the 40th International Conference on
Advanced Ceramics and Composites
January 24–29, 2016
Daytona Beach, Florida