Developments in Strategic Ceramic Materials II
A Collection of Papers Presented at the 40th International Conference on Advanced Ceramics and Composites January 24–29, 2016 Daytona Beach, Florida
Edited by Waltraud M. Kriven Jingyang Wang Yanchun Zhou Dongming Zhu Gustavo Costa
Volume Editors Manabu Fukushima Andrew Gyekenyesi
Copyright © 2017 by The American Ceramic Society. All rights reserved.
Published by John Wiley & Sons, Inc., Hoboken, New Jersey.
Published simultaneously in Canada.
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ISBN: 978-1-119-32178-1 ISSN: 0196-6219
CONTENTS
Preface
Introduction
Geopolymers
Durability Performance of Alkali-Activated Metakaolin, Slag, Fly Ash, and Hybrids
Abstract
Introduction
Experimental Procedures
Results & Discussion
Summary and Conclusion
Acknowledgements
References
MICA Platelet-Reinforced Geopolymer Composites
Abstract
Introduction
Experimental
Results
Conclusion
Acknowledgements
References
Influence of Mix Design Parameters on Geopolymer Mechanical Properties and Microstructure
Abstract
Introduction
Experimental Investigation
Experimental Results and Discussion
Conclusions
Acknowledgements
References
Thermal Performance of Metakaolin-Based Geopolymers: Volume Stability and Residual Mechanical Properties
Abstract
Introduction
Experimental Program
Experimental Results and Discussion
Conclusions
Acknowledgements
References
Effect of Phyllosilicate Type on the Microstructure and Properties of Kaolin-Based Ceramic Tapes
Abstract
Introduction
Materials
Methods
Results and Discussion
Conclusion and Prospects
Acknowledgement
References
Effect of Alkali Cations on the Polycondensation Reaction
Abstract
Introduction
Experimental
Results
Discussion
Conclusions
References
Development of a Mold for Thermoplastics Based on a Phosphate Cement
Abstract
Introduction
Experimental Work
Results and Discussion
Proof of Concept
Conclusions
References
Properties of Cork Particle Reinforced Sodium Geopolymer Composites
Abstract
Introduction
Experimental Procedure
Results and Discussion
Conclusion
Acknowledgement
References
The Role of Alkaline Earth Ions in Geopolymer Binder Formation
Abstract
Introduction
Experimental Part
Results and Discussion
Conclusion
References
Investigations of the Thermally Induced Hydrogen Release of NaBH4 , NH3 BH3 and Their Geopolymer Composites
Abstract
Introduction
Experimental
Results and Discussion
Conclusion
References
IR-Spectroscopic Investigation of Geopolymer and CSH-Phase Stability on Heating Temperature in Post-Fired Building Materials
Abstract
Introduction
Experimental
Results and Discussion
Conclusions
References
Mixed Alkali Regional Metakaolin-based Geopolymer
Abstract
Introduction
Experimental Procedures
Results and Discussion
Conclusions
Acknowledgements
References
Bamboo-Geopolymer Composite: A Preliminary Study
Abstract
Introduction
Materials and Methods
Results and Discussion
Conclusions
Acknowledgements
References
Metakaolin-Based Geopolymer Cements from Commercial Sodium Waterglass and Sodium Waterglass from Rice Husk Ash: A Comparative Study
Abstract
Introduction
Materials and Experimental Methods
Results and Discussion
Conclusion
Acknowledgments
References
Recycling of Grog by Addition into Heavy Clay Ceramic Manufacturing
Abstract
Introduction
Materials and Methods
Results and Discussion
Conclusions
Acknowledgements
References
Virtual Materials Design and Ceramic Genome
Q-State Monte Carlo Simulations of Magnetic Anisotropy Applied to Paramagnetic and Diamagnetic Materials
Abstract
Introduction
The Model
Results
Conclusions
Acknowledgments
References
First Principles Study of Defect Formation in Bulk B6 O
Abstract
Introduction
Computational Details
Results and Discussion
Conclusions
Acknowledgements
References
Modeling of Damage in an MMC with Lamellar Microstructure
Abstract
Introduction
Materials and Experimental
Analytical Modelling
FE Modelling
Results and Discussion
Conclusions and Outlook
Acknowledgement
References
Micro-Computed Tomography Image based Thermo-Elastic Properties Studies of Freeze-Cast MMC
Abstract
Introduction
Materials and Experimental
Material Modelling and Discussion
Conclusions
Acknowledgement
References
Materials for Extreme Environments
Densification and Phase Evolution of SHS Derived Ti2 AlN Active Precursor Powders During Hot Pressing Processes
Abstract
Introduction
Preparation
Results and Discussion
Conclusions
Acknowledgments
References
Max Phase Materials for Nuclear Applications
Abstract
Introduction
Experimental
Results and Discussion
Conclusions
Acknowledgements
References
Analysis of Dynamic Young's Modulus and Damping Behavior of ZrB2 -SiC Composites by the Impulse Excitation Technique
Abstract
Introduction
Experimental Methods
Results and Discussion
Conclusions
Acknowledgements
References
Advanced Ceramic Coatings
Study of Effect of Hafnium Addition on Oxidation Resistance of βNiAl Coatings Prepared by an in-situ Chemical Vapour Deposition Method
Abstract
Introduction
Experimental
Results
TGO
Discussion
Conclusions
Acknowledgments
References
Mass Transfer Mechanism in Mullite Under Oxygen Potential Gradients at High Temperatures
Abstract
Introduction
Experimental
Results and Discussion
Conclusions
Acknowledgements
References
Emerging Technologies— Carbon Nanostructures
SnO2 -Reduced Graphene Oxide Nanocomposite for Ethanol Sensing at Room Temperature
Abstract
Introduction
Experimental
Results and Discussion
Conclusions
Acknowledgements
References
Author Index
EULA
List of Tables
Chapter 1
Table 1 Chemical composition of solid materials (wt%)
Table 2 Mixture proportion of alkali-activated metakaolin (AAMK), fly ash (AAB), slag (AAH) and hybrids in weight ratio
Table 3 Mixture proportions of OPC, modified-OPC, and AAC mortar prisms
Chapter 2
Table 1 Thermal conductivity of geopolymer composites as a function of mica content
Chapter 3
Table 1 Chemical composition of Meta Max (Metakaolin from BASF Co., Germany)
Table 2 Mix proportion of metakaolin geopolymers
Chapter 4
Table I Chemical composition (by weight) of MetaMax (Metakaolin from BASF)
Table II Mix proportion of metakaolin geopolymers
Chapter 5
Table 1 Chemical compositions (wt.%) of the different clays
Table 2 Characteristic sizes and other physical parameters of kaolin, talc and palygorskite
Chapter 6
Table 1 Physical and chemical feature of silicate solutions before and after the addition of hydroxide pellets
Table 2 Physical and chemical features of metakaolin
Chapter 9
Table 1 The chemical compositions of the various geopolymer binders with A= Ca, Mg or Sr
Chapter 11
Table 1 Compressive strength of samples AAMK and AAH
Chapter 12
Table 1 Chemical composition of KA and MKA by XRF
Table 2 Average compressive strength of 25x50-mm tested samples with Weibull parameters
Table 3 Average 4-point flexural strength of 30x12-mm tested samples with Weibull parameters
Chapter 13
Table 1 Third-point loading flexural strength results and Weibull parameters
Chapter 14
Table 1 Chemical composition of Dibo, RHA and PRHA in mass percent
Table 2 Compressive strength of geopolymer cements (MPa), the values of main band on the IR spectra of geopolymer cements (cm-1 ) and mass loss (%)
Chapter 15
Table I Chemical composition of the raw materials (wt %)
Chapter 17
Table I Change in cohesive energy (Δ CE) and Percent Unit Cell Volume Contraction for single and multi-atom 1st , 2nd , 3rd , and 4th nearest neighboring vacancies in B6 O. See Figure 2 for site notation. Note: Bp-intericosahedral is the inter-icosahedral link to a polar boron site from nearest neighboring boron icosahedra and Ochain is the nearest neighboring oxygen to O1
Chapter 18
Table 1
Chapter 20
Table I Phase composition of Ti2 AlN SHS synthesis products
Table II Phase evolution of hot-pressed SHS derived Ti2 AlN powders obtained as a result of synthesis of 3Al + 4 Ti3 Al under 1.5 atm. nitrogen pressure [wt.%]
Table III Phase evolution of hot-pressed SHS derived Ti2 AlN powders obtained as a result of synthesis of 2Al + 4 Ti3 Al under 1.5 atm. nitrogen pressure [wt.%]
Table IV Phase evolution of hot-pressed SHS derived Ti2 AlN powders obtained as a result of synthesis of 2Al + 4 Ti3 Al under 5 atm. nitrogen pressure [wt.%]
Table V Apparent densities of hot-pressed Ti2 AlN materials [g/cm3 ]
Chapter 21
Table 1 The investigated Zr-Al-C starting compositions, sintering temperatures and identified phase assemblies. The majority phases are indicated in bold. The composition of the Zr4 AlC3 , Zr3 AlC2 and Zr2 AlC nominal stoichiometries are presented in the bottom three rows
Table 2 Experimental lattice parameters for the Zr2 AlC and Zr3 AlC2 compounds, as obtained by Rietveld refinement of the XRD spectra
Table 3 Mechanical properties of Nb4 AlC3 and (Nb0.85 ,Zr0.15 )4 AlC3 at room temperature
Chapter 22
Table I Mechanical properties of ZrB2 -SiC composites
Table II Coefficients A0 , A1 and A2 of (3) with T in (°C) and E in (GPa), obtained from the best fits to the experimental data shown in Figure 4. In the last column, the goodness of the fit is given by the coefficient of determination R2
Table III Damping peaks and temperature for each ZrB2 -SiC composite
Chapter 23
Table 1 show an averaged EDS point analysis taken at different locations of coating cross-sections as-deposited condition
List of Illustrations
Chapter 1
Figure 1 Comparison between FTIR spectra of AAC (K0.6 series) before and after the accelerated carbonation test, exposed to CO2 concentration of 3 vol% for 9 days
Figure 2 A comparison between OPC and AAC mortars immersed in H2 SO4 with pH 0.5: weeks, and (c) AAC mortars with AAC coating layer at 11 weeks
Figure 3 AAMK and AAFA mortars (K0.5 and K0.64) immersed in H2 SO4 with pH 0.5: (a) after 2 days, (b) after 9 weeks
Figure 4 AAMK and AAH mortars (K0.5 and K0.64) immersed in H2 SO4 with pH. 0.5: (a) after 2 days, (b) after 9 weeks
Figure 5 AAB and AAB/MK mortars (K0.5 and K0.64) immersed in H2 SO4 with pH 0.5: (a) after 2 days, (b) after 9 weeks
Figure 6 AAH and AAH/MK mortars (K0.5 and K0.64) immersed in H2 SO4 with pH 0.5: (a) after 2 days, (b) after 9 weeks
Chapter 2
Figure 1 Increasing flexure strength with mica content at room temperature, as indicated from left to right
Figure 2 Increase in flexure strength with mica content after 700 °C heat treatment. Samples without mica were too weak to test after heat treatment
Figure 3 Effect of heat treating 20 wt% mica in K-GP composite, with temperatures being read from left to right
Figure 4 Thermal conductivity as a function of mica content. Square symbols indicate 24 h of equilibration, while diamond symbols indicate only 3 h of equilibration
Figure 5 SEM micrograph of pure mica platelets between 100 and 5 microns in diameter
Figure 6 SEM micrograph of 20 weight percent mica in K-GP with no heat treatment
Figure 7 SEM micrograph of 20 wt % mica in K-GP after 1 hour at 700 °C
Figure 8 SEM micrograph of 20 weight percent mica in K-GP after 1 hour at 700°C
Chapter 3
Figure 1 Geopolymer Synthesis
Figure 2 Density of geopolymers (a) Density vs w/solids for different Si/Al ratios (b) Compressive strength Vs density for all the geopolymer samples
Figure 3 Analysis of compressive strength data (a) Plot for compressive strength versus Si/Al (b) Plot for compressive strength versus w/solids
Figure 3 Analysis of the compressive strength data (c) Plot for compressive strength versus Al/Na (d) Plot for compressive strength versus H2 O/Na2 O
Figure 4 SEM images of geopolymers with Si/Al 1.03 and 2.0 observed at magnification level 10k
Chapter 4
Figure 1 Visual observation of metakaolin geopolymer specimens (50 mm cubes) after subject to elevated temperature
Figure 2 The volume shrinkage of geopolymer cube specimens with different Si/Al ratios after exposure to high temperature
Figure 3 Weight loss of cube specimens with different Si/Al ratios when exposed to high temperature
Figure 4 Influences of Si/Al and temperature on microstructure of MK-geopolymers
Figure 5 Residual compressive strength vs Si/Al after different temperature exposures
Figure 6 Cement paste disintegrated at 900°C
Figure 7 Variation in residual density of geopolymers with Si/Al ratio
Chapter 5
Figure 1 Typical structure of (a) kaolinite, (b) talc and (c) palygorskite minerals
Figure 2 Simplified representation of a tape casting set-up and slurry preparation
Figure 3 Thermal analysis diagrams of the starting talc clay
Figure 4 Thermal analysis curves of typical kaolin-palygorskite tapes a) DTA-TG and b) thermodilatometry. Heating rate = 5°C/min under dry air
Figure 5 Biaxial flexural strength of some green and sintered (1100°C) kaolin-palygorskite samples. For each series from left to right: green tape 1.6 mm; sintered tape 1.6 mm; green tape 1 mmm and sintered tape 1 mm
Figure 6 SEM micrographs and open porosity values of the kaolin-palygorskite samples before and after firing at 1100°C
Figure 7 DTA-TG and DTG curves for the K50T50 sample (heating rate = 5°C/min, dry air)
Figure 8 a) Open porosity (from left to right: 900, 1000 and 1100°C) and b) stress to rupture values for some kaolin-talc tapes upon firing (from left to right: K90T10, K50T50 and T100)
Chapter 6
Figure 1 FTIR spectra of (A) SNNa , (B) S1K and (C) S3K solutions before and after the addition of MOH hydroxide pellets
Figure 2 Infrared spectra of [S3K KOH ] mixture at various time
Figure 3 Evolution of the Si-O-M peak position as a function of time for (a) ▄ [SNNa NaOH ], A [S1K KOH ], and o [S3K KOH ] and (b) □ [SNNa KOH ], ▴ [S1K NaOH ], and • [S3K NaOH ]
Figure 4 Evolution of the specific compressive strength (σρ ) values versus the Si molar concentration for the different samples [SxM MOH ] (▄ SNNa NaOH , □ SNNa KOH ▄ S1K NaOH , ▴ S1K KOH , • S3K NaOH , and O S3K KOH )
Chapter 7
Figure 1 View of the digital image correlation (DIC) test setup
Figure 2 XRD diffractograms for partially and fully cured specimens for the three curing regimes, at the right hand side, reference diffractograms are given (http://webmineral.com/data/)
Figure 3 Average linear deformation during 1st heating and cooling cycle (RT - 300°C - RT) for different curing methods. As all specimen shrink only negative deformations are observed
Figure 4 Comparison of tensile stress-strain curves cured at RT and 60°C
Figure 5 (a). The master mold in wooden
Figure 5 (b). Master model covered with frame wax sheet
Figure 6 Workability of topcoat with AEROSIL and Dupont Alesta HR filler
Figure 7 (a). Impregnation of the CSM with
Figure 7 (b). Impregnation of the CSM with topcoat. Vubonite matrix
Figure 8 Matched die TRC mold
Figure 9 Mold placed in the industrial press
Figure 10 Thermoformed Twintex part
Chapter 8
Fig 1 Plot of four-point flexural strength vs. solids loading for cork particle reinforced sodium geopolymer. An increase in flexural strength as solids loading increased was noted
Fig 2 Measured flexure stress vs. flexure strain for a sample in the 60 wt% cork sample group
Chapter 9
Figure 1 (A) The protocol for the synthesis of the geopolymer binder with A = Ca, Mg or Sr (B) The molar composition of different mixtures of ternary Si-Al-(Na+Ca) /O ((•)
Figure 2 (A) The evolution of the FTIR spectrum of sample C1sol (B) The intensity ratio (Si-O-CaO / H2 O) as a function of the nCa /nSi ratio at (•) 0, (▄) 60, (▴) 90 and ▴ 120 min
Figure 3 (A) Thermal analysis curves obtained at 25 and 70°C (B) Mass losses for different samples
Figure 4 Diffractograms of different samples: (A) Anatase 00-021-1272 (B) Calcium aluminum oxide carbonate hydrate 00-041-0219 (Q) Quartz 00-003-0419 (T) Thermonatrite 00-008-0448 (C) Calcite 01-072-1937 (H) Calcium hydroxide 00-033-0268
Figure 5 (A) Infrared spectra at 12 h for samples (a) (b) (B) XRD patterns of the same samples ((Q) Quartz 00-003-0419 (B) hydrated calcium phase 00-041-0219 (T) Thermonatrite 00-008-0448 (C) Calcite 01-072-1937 (M) Magnesium hydroxide 04-011-5938 (S) Strontianite 00-005-0418)
Figure 6 Thermal analyses of different samples
Figure 7 SEM micrographs of (A) (B) and (C)
Chapter 10
Figure 1 TG, dTG (dashed line) and heat flow curves of AB-G heated under synthetic air to 300°C
Figure 2 TIR spectra of (a) AB and (b) AB-G in KBr matrix. The IR modes of BH4 − in KBr matrix are indicated
Figure 3 TIR spectra of (a) AB and (b) AB-G in KBr in the presence of NaNO3 tracer from 25 to 180°C, in the spectral range between 600 and 1800 cm-1 . Asterisks indicate the BH4 − peak at 1123 cm-1 (ν 4 ) and the NH2 deformation mode at 1566 cm-1
Figure 4 Variation of the integral intensity of ν 2 (NO3 − ) of NaNO3 tracer for AB (stars) and AB-G (squares) as a function of the temperature in the TIR spectra using NaNO3 tracer, in comparison with the thermal behavior of a reference NaNO3 /KBr pellet (open circles). The heat flow curve of AB-G (dashed line) is overlaid for comparison
Figure 5 TG/DTA of SB-G under He (upper graph, dashed line is for dTG) and under synthetic air (lower graph, solid and dash-dotted lines are for the measurements performed with and without pre-evacuating the samples before the heating runs, respectively)
Figure 6 TG/DTA of SB under synthetic air (upper graph, solid and dash-dotted lines are for the measurements performed with and without pre-evacuating the samples before the heating runs, respectively) and under He (lower graph, dashed line is for dTG)
Figure 7 TIR spectra of SB/KBr (at the left side). At the right side, the corresponding spectra are zoomed between 1200 and 1700 cm-1 . Asterisks are used to follow the intermediary peak at 1575 cm-1 . Dashed lines are for the TIR spectra between 400 and 1800 cm-1 in the presence of NaNO3
Figure 8 Integrated intensities (Int. I) of B3 O6 3 − (triangles), BH4 − (circles), NO3 − (filled-square) in TIR of SB/KBr in the presence of NaNO3 tracer. Non-filled squares are for the reference pellet NaNO3 /KBr. Integral intensities are for the TIR spectra of samples cooled down to 25°C from T as denoted (lines are guide for eyes)
Chapter 11
Figure 1 IR-absorption spectra (KBr-method) of hardened cement pastes CEM I 52,5 N (= CEM I), CEM III/B 42,5 N (=CEM III), CEM I with the addition of 50% H (CEM I_H), unheated and heated at 600°C (gray)
Figure 2 XRD pattern of hardened cement paste CEM I 52,5 N (= CEM I) unheated and at 600°C (gray) and their difference as denoted. Some peak positions has been marked (CSH* by arrows)
Figure 3 IR absorption spectra (KBr-method) of CEM I 42,5 R based series of cement pastes
Figure 4 IR absorption spectra (ATR method) in relative transmissivity of CEM I 42,5 R based series of cement pastes
Figure 5 Density of states peak maximum (DOSPM) of the asymmetric Si-O vibration (ATR-method) of series of samples as denoted
Figure 6 Density of states peak maximum (DOSPM) of the asymmetric Si-O vibration (ATR-method) of series of mortars compared to their compressive strength behavior
Figure 7 Density of states peak maximum (DOSPM) of the asymmetric Si-O vibration of series of concretes (Micro-IR in transmission mode of probes pressed between diamond plates)
Figure 8 XRD pattern of AAMK and AAH (a, right) and AAH compared to CEM III and CEM I (b, left). Details are given in the text
Figure 9 IR absorption spectra (KBr-method) of 3 examples of AAH samples, unheated, 600°C and 800°C heated each (AAH1 with WG1 , AAH2 and AAH3 with WG2 , compare experimental)
Figure 10 IR absorption spectra of AAMK samples unheated (two spectra) and heated at 800°C taken from a solid piece and fine material after the strength measurement
Chapter 12
Figure 1 (A) Water-treated bamboo culms; (B) water-treated BF1W reinforcement; (C) washed BF4W reinforcement just before use
Figure 2 (A) Potassium-Sodium water glass K75Na25-WG; (B) Amazonian metakaolin MKA
Figure 3 Cylindrical compressive 25x50-mm specimens MKA76 GPC
Figure 4 Four-point flexural plate and specimen MKA76-BF GPC
Figure 5 TGA for KA
Figure 6 (A) KA and (B) MKA XRD, 2Θ 5°-80°
Figure 7 SEM of K75Na25-MKA76 GP
Figure 8 SEM of K75Na25-MKA76-BF4W GPC showing imprints of the pulled out BFs
Figure 9 Typical stress-strain curve for BF4W GPC tested in bending. Strain units are in percent
Chapter 13
Figure 1 Green bamboo (a ) culms, (b ) chips and (c ) fiber bundles
Figure 2 Bamboo-reinforced geopolymer composite (a ) plate and (b ) tested specimens
Figure 3 SEM micrographs of bamboo-reinforced K-based geopolymer composite tested specimen, showing gaps and crack propagation in back scattered composite (BEC) mode, 230x and BEC mode, 150x
Figure 4 SEM micrographs of untreated Guadua BF, showing starch (small-round particles) in the parenchymal cells in secondary electron (SEI) and back scattered (BES) modes, 500x
Figure 5 Stress-strain curves for bamboo-reinforced K-based geopolymer composite tested in four-point bending
Figure 6 Weibull plot for flexural strength data of bamboo-reinforced geopolymer composite
Figure 7 XRD pattern of bamboo-reinforced geopolymer composite
Chapter 14
Figure 1 X-ray pattern of metakaolin, MK. (I, A and Q denote peaks of illite, anatase and quartz respectively)
Figure 2 X-ray patterns of rice husk ash (RHA) and pure rice husk ash (PRHA)
Figure 3 IR spectra of rice husk ash (RHA) and pure rice husk ash (PRHA)
Figure 4 IR spectra of metakaolin (MK) and quartz subtracted (MK-0.25 quartz) in comparison to quartz
Figure 5 ATR-IR spectra of sodium waterglass (S1, S2 and S3)
Figure 6 XRD patterns of geopolymers cements Geo1, Geo2, Geo3. A and Q denote peaks of anatase and quartz respectively
Figure 7 Difference XRD patterns of samples as denoted
Figure 8 IR absorption spectra of samples Geo1, Geo2 and Geo3 at 28 days
Figure 9 Evolution of the values of compressive strength as a function of mass loss and the values of the wavenumber of the main bands of geopolymer cements Geo1, Geo2 and Geo3
Figure 10 Difference IR spectra of samples as denoted
Figure 11 TG curves of geopolymers cements Geo1, Geo2, Geo3
Chapter 15
Figure 1 XRD patterns of the raw materials. A: amphibole; K: kaolinite; M: micaceous mineral; Q: quartz
Figure 2 Particle size distribution of the raw materials
Figure 3 DTA/TG curves of the grog
Figure 4 Prognostic of the extrusion stage through the Atteberg's plasticity limits14
Figure 5 Linear shrinkage of the compositions
Figure 6 Correlations among amount of grog incorporated and increased linear fired shrinkage and decreased linear dried shrinkage
Figure 7 Water absorption and flexural rupture strength of the compositions
Chapter 16
Figure 1 Magnetic anisotropy between grains ρ 1 and ρ 2 promotes grain boundary mobility in the direction of the largest free energy; in this case towards grain ρ 1
Figure 2 Magnetic field and c-axis vectors relative to the rolling, transverse and normal directions
Figure 4 Grain growth contours at t=0 and t=200 MCS for WMF (a,b) and WOMF (d,e) representative hexagonal polycrystalline materials; Also shown is the WMF/WOMF evolutions of average grain size (c) and total grain boundary energy (f)
Figure 5 WOMF/WMF misorientation angle distributions corresponding to Case 1 at t = 200 MCS for representative hexagonal and cubic polycrystalline materials
Figure 6 WOMF/WMF Ф distributions corresponding to Case 1 at t = 200 MCS for representative hexagonal and cubic polycrystalline materials
Figure 7 WOMF/WMF Misorientation distributions corresponding to Case 2 at t = 200 MCS for representative hexagonal and cubic polycrystalline materials
Figure 8 WOMF/WMF Ф distributions corresponding to Case 2 at t = 200 MCS for representative hexagonal (a) and cubic (b) polycrystalline materials
Chapter 17
Figure 1 Crystal structure of pristine 2x2x1 B6 O unit cell. Left: off-axis view; Right: perpendicular to c-axis; B and O atoms are pink and red respectively
Figure 2 Site Notation for single boron icosahedra from unit cell identifying vacancy locations which correspond to notation in Table I
Figure 3 ELF iso-slices through different atomic planes of pristine B6 O with (right) and without (left) a single vacancy. (a) Slice perpendicular to c-axis through O1 in B6 O (Left) and through O1 vacancy (Right) (b) Slice along <110> through atomic plane containing Ochain -O1 -Be1 in B6 O (Left) and with O1 vacancy (Right) (c) Slice perpendicular to c-axis through diameter of icosahedra in B6 O (Left) and with Be6 vacancy (Right) (d) Slice through Ochain -Ochain -Be6 in B6O (Left) and with Be6 vacancy (Right) (e) Slice through Bp - Bp - Bp plane within icosahedra in B6O (Left) and with Be6 vacancy (Right) (f) Slice through Bp - Bp - Bp plane within icosahedra in B6O (Left) and with Bp1 vacancy (Right) (g) Slice through plane containing inter-icosahedra Bp-Bp1 bonds in pristine B6O (Left) and with Bp1 vacancy (Right). Red indicates areas where ELF = 1, whereas ELF = 0 for the dark blue region. The atoms and bonds that are shown as connected balls and sticks exist in the plane slice, whereas the atoms displayed as lines are exterior. Pink and red balls represent boron and oxygen respectively
Figure 4 Local defect structure and relative defect energies for single atom and multi-atom vacancies. See Figure 3 for notation explanation and Table I for corresponding unit cell contractions and changes in cohesive energy
Chapter 18
Figure 1 SEM micrographs showing the progressive damage evolution in one region in single-domain sample at different applied stresses. A compressive load was applied at 45° to the domain orientation (=horizontal direction). The actual stress–strain plot is shown in the image. The micrographs correspond to the locations marked by the numbers on the stress–strain plot
Figure 2 a) Schematics showing a composite sample with multiple cracks in the ceramic layer; b) representative segment bounded by two cracks without crack widening; c) representative segment bounded by two cracks with crack widening 2l
Figure 3 FE model of a quarter of the representative segment with thicknesses 2hc and hm of the ceramic and metallic layers. 2s is the crack spacing und 2l is the crack widening
Figure 4 Normalized axial stress in the ceramic layer as a function of co-ordinate x2 for a range of crack spacing to layer thickness ratios as predicted by the analytical model: a) no widening Dw = 0; b) with relative crack widening Dw = 10%
Figure 5 Axial stress distribution in the cracked ceramic layer for three crack half-spacing to layer thickness ratios: a) s/hc =1.3 ; b) s/hc =1.0; c) s/hc =0.7. No crack widening
Figure 6 Axial stress distribution in the cracked ceramic layer for s /hc = 1.3 : a) without crack widening Dw = 0; b) with relative crack widening Dw = 10%; c) with relative crack widening Dw =15%
Figure 7 Axial stress distribution in the ceramic layer for s / hc = 1.0: a) without crack widening Dw =0; b) with relative crack widening Dw = 10%; c) with relative crack widening Dw =1 5%
Figure 8 Shear stress distribution in the cracked ceramic layer for three crack half-spacing to layer thickness ratio s/hc =1.3: a) without crack widening Dw = 0; b) with relative crack widening Dw = 10%; c) with relative crack widening Dw =15%
Chapter 19
Figure 1 μCT pictures for 2D and 3D model with a) 1003 voxels (single domain structure) and b) 2503 voxels (poly domain structure); c) ABAQUS finite element model 100x100x100 elements
Figure 2 Variation of the ceramic content along the axes a) Z and b) Y; c) normal and d) shear components of the stiffness tensor
Figure 3 Comparison of experimental measurements9 with modeling results (3D model)
Figure 4 3D Microstructure view for different specimens used for thermal studies: a) T3, b) T4, c) T5 consisting of 375x375x75 voxels; 2D singe slices for d) T3, e) T4, f) T5 (in this image ceramic is white) (750x750 grey)
Figure 5 a) Heat conductivity calculated using 2D and 3D models of the microstructure (see Figure 4), b) thermal expansion calculated using 2D and 3D models of the microstructure (see Figure 1)
Figure 6 Experimental and modeling results for thermal conductivity of the ceramic preform for following models: 1) 375x375x75 voxels; 31% alumina; 2) 250x250x250 voxels ; 44% alumina and comparing with analytical models
Figure 7 Experimental and modeling results for thermal conductivity of the composite (31% alumina). The experimental measurements were provided parallel and perpendicular to the freeze-casting direction. Calculations were provided using FE for the microstructures T3 and T5 (see Figure 4)
Chapter 20
Figure 1 XRD pattern of the large Ti2 AlN powders obtained by SHS reaction 2 under 5 atm. nitrogen pressure
Figure 2 Morphology of SHS derived Ti2AlN powders
Figure3 XRD pattern of the Ti2 AlN sample hot-pressed at 1300°C
Chapter 21
Figure 1 Ternary Zr-Al-C phase diagram showing the different Zr4 Alw Cx (in blue) and Zr3 Aly Cz (in black) starting compositions (see Table 1), together with the Zrn+1 AlCn reference compositions (in red)
Figure 2 XRD patterns of the Zr4 Alw Cx ceramics hot pressed at 1550°C (a) and Zr3 Aly Cz ceramics hot pressed at 1525°C (b)
Figure 3 HRTEM images of Zr3 AlC2 (a) and Zr2 AlC (b) combined with a mapped atomic stacking (green = Zr, blue = Al, grey = C)
Figure 4 Lattice parameters of (Nb1-x ,Zrx )4 AlC3 as function of the composition (a) and backscattered electron (BSE) detector images of the microstructure of Nb4 AlC3 and (Nb0.85 ,Zr0.15 )4 AlC3 (b). The black dots are Al2 O3 particles
Figure 5 The dynamic elastic properties of Nb4 AlC3 and (Nb0.85 ,Zr0.15 )4 AlC3 as function of temperature plotted together with the temperature dependence of the 4-point flexural strength of (Nb0.85 ,Zr0.15 )4 AlC3
Chapter 22
Figure 1 Schematic of the sintering cycles (S1 and S2) used during PECS
Figure 2 Particle morphology of commercial (a) and self-synthesized (b) ZrB2 powders
Figure 3 Backscattered SEM micrographs of ZrB2 -SiC ceramics, CZS-S1, SZS-S1(a) and CZS-S2, SZS-S2(b) prepared by sintering cycle S1 and S2 respectively
Figure 4 Temperature dependent Young's modulus and damping spectra of ZrB2 -SiC composites prepared by sintering cycle S1 (a) and S2 (b)
Chapter 23
Figure 1a - f shows the cross-sections of the undoped βNiAl and Hf-βNiAl samples in as-deposited condition with EDS line profile across the thickness and (g) corresponding XRD spectra of the coatings
Figure 2 shows the TGO morphologies; (a) - (c) simple βNiAl and (d) - (f) Hf-βNiAl. Typical ridge morphology, thick and multiphase TGO is observed in simple βNiAl while similar ridge and essentially single phase TGO is seen in Hf-βNiAl
Figure 3 shows the TGO growth rates and stresses of both doped and undoped coatings after oxidation (at 1150oC for 100 hours in air)
Chapter 24
Figure 1 Effect of Po2 in the upper chamber on the oxygen permeability constants (PL·Sgb -1 ) of polycrystalline mullite and Al2 O3 at 1873 K. The Po2 in the lower chamber was constant at 1 Pa
Figure 2 SEM micrograph of the Po2 (hi) surface and a cross-section of a mullite wafer exposed to a Po2 (hi)/Po2 (lo) ratio of 105 Pa/1 Pa at 1873 K for 10 h
Figure 3 Equilibrium partial pressures Pi of the primary volatile species for mullite under a total pressure of 105 Pa
Figure 4 Arrhenius plots of the |Ai |·Sgb -1 values of polycrystalline mullite wafers exposed to Po2 (hi)/Po2 (lo) ratios of 1 Pa/(10-9 –10-6 ) Pa for oxygen and 105 Pa/1 Pa for Al, respectively
Figure 5 Oxygen permeability constants (PL·Sgb -1 ) of polycrystalline mullite as functions of the Po2 (hi)/Po2 (lo) ratio at 1873 K. Po2 (lo) was held constant at 10-6 Pa
Figure 6 SEM micrograph of a cross-section of the Po2 (hi) surface of a mullite wafer exposed to a Po2 (hi)/Po2 (lo) ratio of 105 Pa/10-6 Pa at 1873 K for 10 h
Figure 7 SEM micrograph of a cross-section in the vicinity of the Po2 (lo) surface of a mullite wafer exposed to a Po2 (hi)/Po2 (lo) ratio of 105 Pa/10-6 Pa at 1873 K for 10 h
Chapter 25
Figure 1 XRD patterns of (a) graphite oxide (GO), (b) SnO2 -RGO nanocomposite
Figure 2 FTIR spectrum of (a) graphite oxide (GO), (b) SnO2 -RGO nanocomposite
Figure 3 FESEM images of SnO2 -RGO of (a,b) low magnification, (c) high magnification. (d) EDS spectrum of SnO2 -RGO
Figure 4 (a) TEM image, (b) HRTEM image, and (c) SAED pattern of SnO2 -RGO sample
Figure 5 Response of SnO2 -RGO as function of ethanol concentration at room temperature
Figure 6 Responses of SnO2 -RGO to ethanol and methanol (1,000 ppm) at room temperature
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This CESP proceedings issue contains a total of 25 contributions from select symposia held during the 40th International Conference on Advanced Ceramics and Composites (ICACC), in Daytona Beach, FL, January 24–29, 2016.
The wide range of topics in this issue were presented in the following Symposia and Focused Sessions:
Symposium 2—Advanced Ceramic Coatings for Structural, Environmental, and Functional Applications
Symposium 10—Virtual Materials (Computational) Design and Ceramic Genome
Symposium 12—Materials for Extreme Environments: Ultrahigh Temperature Ceramics and Nanolaminated Ternary Carbides and Nitrides
Focused Session 1—Geopolymers and Chemically Bonded Ceramics
Emerging Technologies Symposium on Carbon Nanostructures
The editors wish to thank the symposium organizers for their time and efforts, the authors and presenters for their contributions; and the reviewers for their valuable comments and suggestions. In addition, acknowledgments are due to the officers of the Engineering Ceramics Division of The American Ceramic Society and the 2016 ICACC program chair, Andrew Gyekenyesi, for their support. It is the hope that this volume becomes a useful resource for academic, governmental, and industrial efforts.
WALTRAUD M. KRIVEN, University of Illinois at Urbana-Champaign, USA JINGYANG WANG, Institute of Metal Research, Chinese Academy of Sciences, China YANCHUN ZHOU, Aerospace Research Institute of Material & Processing Technology, China
DONGMING ZHU, NASA Glenn Research Center, USA GUSTAVO COSTA, NASA Glenn Research Center, USA
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 structural, functional, and nanoscopic ceramics, composites, and other emerging ceramic materials and technologies. This prestigious conference has been organized by the Engineering Ceramics Division (ECD) of The American Ceramic Society (ACerS) since 1977. This year's meeting continued the tradition and added a few grand celebrations 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 materials science developments at the atomic level and macro level structural applications. Papers addressed material, model, and component development and investigated the interrelations between the processing, properties, and microstructure of ceramic materials.
The 2016 conference was organized into the following 17 symposia and 5 Focused Sessions:
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 11 Materials for Extreme Environments: Ultrahigh Temperature Ceramics (UHTCs) and Nano-laminated
Symposium 12 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
Focused Session 7 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 proceedings were possible thanks to the professional staff of ACerS and the tireless dedication of many ECD members. We would especially like to express our sincere thanks to the symposia organizers, session chairs, presenters and conference attendees, for their efforts and enthusiastic participation in the vibrant and cutting-edge conference.
ACerS and the ECD invite you to attend the 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