Advances in Materials Science for Environmental and Energy Technologies VI E-Book

• Herausgeber: John Wiley & Sons
• Kategorie: Fachliteratur
• Serie: Ceramic Transaction Series
• Sprache: Englisch

Seitenzahl: 394

Veröffentlichungsjahr: 2018

Beschreibung

An excellent one-volume resource for understanding the most important current issues in the research and advances in materials science for environmental and energy technologies This proceedings volume contains a collection of 20 papers from the 2016 Materials Science and Technology (MS&T'16) meeting held in Salt Lake City, UT, from October 24-27 of that year. These conference symposia provided a forum for scientists, engineers, and technologists to discuss and exchange state-of-the-art ideas, information, and technology on advanced methods and approaches for processing, synthesis, characterization, and applications of ceramics, glasses, and composites. Topics covered include: the 8th International Symposium on Green and Sustainable Technologies for Materials Manufacturing Processing; Materials Issues in Nuclear Waste Management in the 21st Century; Construction and Building Materials for a Better Environment; Materials for Nuclear Applications and Extreme Environments; Nanotechnology for Energy, Healthcare, and Industry; and Materials for Processes for CO2 Capture, Conversion and Sequestration. * Logically organized and carefully selected articles give insight into advances in materials science for environmental and energy technologies. * Incorporates the latest developments related to advances in materials science for environmental and energy technologies Advances in Materials Science for Environmental and Energy Technologies VI: Ceramic Transactions Volume 262 is ideal for academics in mechanical and chemical engineering, materials and or ceramics, chemistry departments and for those working in government laboratories.

Leseprobe

Advances in Materials Science for Environmental and Energy Technologies VI

Ceramic Transactions, Volume 262

Edited by

Tatsuki Ohji

Josef Matyáš

Henry Colorado

Raghunath Kanakala

This edition first published 2017© 2017 The American Ceramic Society

All rights reserved. No part of this publication may be reproduced, stored in a retrieval system, or transmitted, in any form or by any means, electronic, mechanical, photocopying, recording or otherwise, except as permitted by law. Advice on how to obtain permission to reuse material from this title is available at http://www.wiley.com/go/permissions.

The rights of Tatsuki Ohji, Josef Matyáš, Henry Colorado, and Raghunath Kanakala to be identified as the authors of the editorial material in this work have been asserted in accordance with law.

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Library of Congress Cataloging-in-Publication Data is availableISBN: 9781119423768ISSN: 1042-1122

Cover design by Wiley

Contents

Preface

GREEN AND SUSTAINABLE TECHNOLOGIES FOR MATERIALS MANUFACTURING AND PROCESSING

Titania Nanosheet Production by an Inexpensive Green Process

Green Synthetic Method for Synthesis of Calcium Molybdate Based on a Bimetallic Complex

Controlling Factors Aiming for High Performance SiC Polycrystalline Fiber

Extrusion and Tape Casting Based Production of New Lightweight Kiln Furniture with Non-Planar Surface

Development of Stoneware Body Formulation Suitable For Fast Firing

Comparative Study on the Microstructure Evolution of Semicoke and Lump Coal under High Temperature

Carbon Structure in Blast Furnace Dusts Characterized by Raman Spectroscope and Its Links with Combustion Reactivity

CONSTRUCTION AND BUILDING MATERIALS FOR A BETTER ENVIRONMENT

Portland Cement Paste Blended with Pulverized Coconut Fibers

Mechanical Properties of Jute Fiber Reinforced Geopolymers

Calcium Alumínate Cements Subject to High Temperature

Aggregate Optimization in Concrete using the Viterbo Method

MATERIALS ISSUES IN NUCLEAR WASTE MANAGEMENT IN THE 21ST CENTURY

Xtractite: An Inorganic Ion-Exchange Material for Sorption of Radionuclides

Effect of Carbonate Concentration on the Dissolution Rates of UO

2

and Spent Fuel—A Review

Volumetrically-Stabilized Pyrochlore Waste form using Co-Doping

Integrated Research Program Overview on the “Innovative Approaches to Marine Atmospheric Stress Corrosion Cracking Inspection, Evaluation and Modeling in Used-Fuel Dry Storage Canisters”

SCC Detection and Life Prediction for Nuclear Waste Management 165 using PGAA and NAA

MATERIALS FOR NUCLEAR APPLICATIONS AND EXTREME ENVIRONMENTS

Reducing Risks in Nuclear Power Plants Operation by using FeCrAl Alloys as Fuel Cladding

Annular Accident Tolerant Fuel with Discs and Rod Inserts

NANOTECHNOLOGY FOR ENERGY, ENVIRONMENT, ELECTRONICS, AND INDUSTRY

Nanocarbon-Infused Metals: A New Class of Covetic Materials for 207 Energy Applications

MATERIALS AND PROCESSES FOR CO

2

CAPTURE, CONVERSION, AND SEQUESTRATION

The Study of Catalysts Based on Intermetallic NiAl Alloys

EULA

List of Illustrations

Titania Nanosheet Production by an Inexpensive Green Process

Figure 1. X-Ray Powder Diffraction Pattern of Titanium Nanosheet Precipitate with the ICDD Diffraction Pattern File for Anatase in Grey.

Figure 2. TEM images of (A) titanium colloid nanosheets, (B) titanium colloid nanosheets with visible lattice fringes, (C) precipitated titanium nanosheets with visible lattice fringes, and (D) precipitated titanium nanosheets embedded and sectioned

Figure 3. (A) Distribution of Height Measurements of (A) Titanium Colloid Nanosheets (B) Precipitated Titanium Nanosheets (C) Distribution of Diameter Measurements of Precipitated Titanium Nanosheets

Figure 4. Atomic Force Microscopy Images of Titanium Colloid Nanosheets (Left) and Precipitated Titanium Nanosheets (Right)

Figure 5: Raman Spectrum of Precipitated Anatase Phase Titanium Nanosheets

Figure 6. FT-IR Spectrum of Precipitated Titanium Nanosheets in a KBr pellet

Figure 7. Dynamic Light Scattering Measurements of the Colloid Titanium Nanosheets (Left) and the Precipitated Titanium Nanosheets (Right)

Figure 8. Plot of (αE

phot

)

2

versus E

phot

for a direct band gap transition. Colloid Titanium Nanosheets (Lower Curve) and the Precipitated Titanium Nanosheets (Higher Curve)

Green Synthetic Method for Synthesis of Calcium Molybdate Based on a Bimetallic Complex

Figure 1. Crystal Structure of CaMoO

4

.

Figure 2. Molybdenyl/ Doubly-Deprotonated 2-Hydroxyisobutyrate Anionic Complex

Figure 3. Thermal Ellipsoid Plot of Structure

Figure 4. Packing Diagram

Figure 5. TGA Trace of the CaMoO

4

Precursor (5 °C/min heating rate).

Figure 6. Proposed Decomposition Pathway of Single Source Precursor

Figure 7. XRD Pattern for CaMoO

4

Derived from the Precursor at 450°C. Grey bars are the ICDD PDF File # 01-077-2238 for CaMoO

4

Controlling Factors Aiming for High Performance SiC Polycrystalline Fiber

Fig. 1 Historical flow of the development of polymer-derived SiC fibers

Fig. 2 The fine structure of the first generation and the second generation

Fig. 3 Production process of the SiC-polycrystalline fiber

Fig. 4 Morphological changes during the further heat-treatment

Fig. 5 Self-forming and self-consuming “

Just-in-time

Reactor system”

Fig. 6 A new process using the “Just-in-time Reactor system

Fig. 7 Improved result concerning the residual carbon using the “

Just-in-time

Reactor system”

Extrusion and Tape Casting Based Production of New Lightweight Kiln Furniture with Non-Planar Surface

Figure 1. New lightweight kiln furniture with integrated hole in top surface - green state - 320 × 250 × 23 mm

3

.

Figure 2. Stack of sintered new lightweight kiln furniture - each 200 × 200 × 12 mm

3

.

Figure 3. Combination of deep-drawn green tapes and machined extrudates forms new lightweight kiln furniture with non-planar surfaces.

Figure 4. Schema of deep drawing process before (1) and after drawing (2) a sample.

Figure 5. Developed test unit to research the deep drawing process for ceramic green tapes.

Figure 6. Green tapes with grid pattern with a mesh size of 2x2 mm before (1) and after deep-drawing (2).

Figure 7. CAD-drawing of half-spherical stamp used for deep drawing tests.

Figure 8. Deep drawing process by using a spherical stamp (d=60 mm) (left), visualization of deformation (middle) and cracking (right).

Figure 9. Force-displacement curves for deep drawing green tapes (60 vol.-%) at different velocities.

Figure 10. Measured forces against time to determine the relaxation for different drawing depth.

Figure 11. Tensile force against draw depth depending on the solid content; all tapes with a thickness of 400 μm.

Figure 12. Deep drawn green tape with a grid pattern (left) and digitalized image of a 3D-scan and investigated elongation for the whole structure (Vialux GmbH).

Figure 13. Defect-free sintered tapes formed by deep drawing with different stamps.

Comparative Study on the Microstructure Evolution of Semicoke and Lump Coal under High Temperature

Figure 1. The equipment for the pyrolysis experiment

Figure 2. The pore size distribution of lump coal at different reaction time

Figure 3. The pore size distribution of semicoke at different reaction time

Figure 4. The results of XRD test of lump coal and semicoke at different reaction time

Figure 5. The change rule of crystalline structure parameters of samples with the reaction time

Figure 6. The maceral changes of lump coal and semicoke with reaction time

Carbon Structure in Blast Furnace Dusts Characterized by Raman Spectroscope and Its Links with Combustion Reactivity

Figure 1. the first-order region Raman spectra and fitting bands for each of carbonaceous substance in samples

Figure 2. Conversion and conversion rate profiles of carbon in dusts and treated coke at the heating rate of 5K/min.

Portland Cement Paste Blended with Pulverized Coconut Fibers

Figure 1: a) and b) Coconut fiber images, c) coconut fiber FTIR

Figure 2: SEM images for a) Cement paste, b) 1wt% of coconut fiber, c) 5wt% of coconut fiber, d) 10wt% coconut fiber

Figure 3: Compressive strength for the samples

Figure 4: a) Compressive strength, b) density

Mechanical Properties of Jute Fiber Reinforced Geopolymers

Figure 1. Particle size distribution curves.

Figure 2. (a) Schematic drawing of the acrylic mold and (b) composite manufacturing process.

Figure 3. Setup for: (a) compression tests; and (b) tensile tests.

Figure 4. Setup for four-point bending tests.

Figure 5. DRX of: a) silica fume; b) metakaolin; c) blast furnace slag.

Figure 6. Compressive Stress × Strain curves of F3.0-100MK, F3.9-80MK20SF and F3.9-

Figure 7. Tensile Stress × Strain curves of the F3.0-100MK, F3.9-80MK20SF and F3.9-60MK40BFS composites.

Figure 8. Composites submitted to tensile tests showing different patterns of cracking.

Figure 9. Flexural Strength × Deflection curves of the F3.0-100MK, F3.9-80MK20SF and F3.9-

Calcium Alumínate Cements Subject to High Temperature

Figure 1a. Density mean values for different sample compositions.

Figure 1b. Typical curves for Compression for samples exposed at 500 °C for 1h.

Figure 2.a) SEM Powder CAC 52wt% AI

2

O

3

, b) SEM Powder CAC 71wt% AI

2

O

3

.

Figure 3. SEM images for CAC pastes, a) 52wt% of Al

2

O

3

- w/c=0.4; b) 52wt% of Al

2

O

3

- w/c=0.5; c) 71wt% of Al

2

O

3

- w/c=0.4; d) 71wt% of Al

2

O

3

- w/c=0.5.

Figure 4a. Images of CAC pastes exposed at room temperature

Figure 4b. Images of CAC pastes exposed at 500 °C

Figure 5. SEM images for CAC pastes exposed at high temperature (1000 °C)

Aggregate Optimization in Concrete using the Viterbo Method

Figure 1. Granulometry curves for (a) fine sand, (b) % aggregate”.

Figure 2. Weight and absorption for (a) sand, (b) 3/4” gravel aggregates.

Figure 3. Air void content as a function of the sand:gravel ratio.

Figure 4. Settlement vs W/C ratio Figure 5 summarizes the different experiments for general use cement after 14, 21, and 28 days of curing, with W/Cs of a) 0.60, b) 0.62, c) 0.63 and d) 0.65. All these tests were conducted in order to estimate the adequate water content.

Figure 5. Samples fabricated at different curing times for W/C ratios of a) 0.60, b) 0.62, c) 0.63 and d) 0.65, all for general use cement.

Figure 6. Compressive strength for mortar samples to determine A and V factors for the cement after 28 days of curing a) general use, b) structural use Portland cement. Samples were fabricated at a W/C of 0.485.

Figure 7. Verifications for cements with (a) G. U. and (b) S. U.

Xtractite: An Inorganic Ion-Exchange Material for Sorption of Radionuclides

Figure 1. Concentration of Uranium Versus Time for Uptake by Excess Xtractite.

Figure 2. Q

t

Versus Time for Uptake of Uranium by Xtractite

Figure 3. Pseudo Second Order Fit of Uranium Uptake Data

Figure 4. Ratio of Uptake Capacity of Xtractite to that of Dowex 650C

Figure 5. Maximum Uptake of Strontium from Various Waters by Xtractite

Effect of Carbonate Concentration on the Dissolution Rates of UO

2

and Spent Fuel—A Review

Figure 1. Measured and calculated solubilities of UO

2

(am) as a function of Eh under various carbonate solutions

9

: (a) concentration of uranium passed through a ultrafilter with pore size of molecular weight cut-off of 10

4

(10 kDa); and (b) concentration of uranium calculated using JAEA’s thermodynamic database (JAEA-TDB)

10

and a geochemical calculation program PHREEQC.

11

Reprinted and modified with permission of the Atomic Energy Society of Japan.

Figure 2. Fuel dissolution rates taken from the uranium fraction of the inventory in the aqueous phase (FIAP) obtained during wash cycles and corrosion of the spent fuel pellet K8 under 3.2 bar H

2

overpressure (FIAP data taken from Carbol et al. 23) (reprinted from Ref. 5)

Figure 3. Dissolution rate of

233

U-doped UO

2

under various conditions (data from Ollila

24

).

Figure 4. Time dependence of the cumulative fuel dissolution calculated from the dissolution rates evaluated in the foreign countries listed in Table I (reprinted from Ref 5).

Figure 5. Collected dissolution rates of UO

2

and SF as a function of [C]

T

. The solid and dashed lines represent the best estimated and the lower / upper limit values of the dissolution rate of 10

−7

y

−1

. See text for detail.

Volumetrically-Stabilized Pyrochlore Waste form using Co-Doping

Figure 1. Cell volume of co-doped Nd

2-x

(Sm, Pr)

x

Ti

2

O

7

Figure 2. XRD pattern overlay of undoped and co-doped Nd

2

Ti

2

O

7

Integrated Research Program Overview on the “Innovative Approaches to Marine Atmospheric Stress Corrosion Cracking Inspection, Evaluation and Modeling in Used-Fuel Dry Storage Canisters”

Figure 1. Project Team Expertise and Disciplines.

Figure 2. CISCC Analysis and Inspection Path

Figure 3. Conditions of SCC initiation and growth

Figure 4. Database Structure

Figure 5. Modeling of mockup welding procedure with finer meshes near weldments (a) and (b), and schematic drawing of the mockup (c) with the rectangular blocks highlighting the locations of microstructural characterization; (d) Multi-pass bead morphology of weldment.

Figure 6. Residual stresses in longitudinal weld centerline as a function of mockup depth obtained from modeling and experimental measurements, respectively.

Figure 7. Imaging four points bend specimen

Figure 8. Calculated stress distribution in of four-points bending specimen

Figure 9. (a) A CAD model showing design of the corrosion chamber and (b) a photograph showing the corrosion chamber built following the CAD design shown in (a).

Figure 10. Schematic view of in-situ X-ray synchrotron tomography experiment

Figure 11. (a) Experimental result of acoustic wave focusing on an aluminum plate superimposed on a photograph of the sample. (b) Photograph of a stainless steel sample with SCC. (c) TREND image of SCC.

Figure 12. Images of the SCCs under an optical microscope, along with spectra of the particle velocity measured for 24 source amplitudes around the fourth resonance mode of vibration of the sample: (a) pristine sample; (b) sample with SCC.

SCC Detection and Life Prediction for Nuclear Waste Management 165 using PGAA and NAA

Figure 1. Typical Canister-Based Storage System

.

Figure 2. Cross-Section of the 24 Unit Spent Fuel System Modeled in MCNP6.

Figure 3. Quarterly Cross-Section View of a Typical PWR Fuel Storage System.

Figure 4. Background Signal – No Chloride Present.

Figure 5. 7.41 MeV Gamma Signal from the Decay of Cl-36.

Figure 6. 7.41 MeV Signal from Cl-36, as a Function of Chlorine Amount, Alongside Background Signal at Outside Surface of Concrete Overpack.

Figure 7. 6.11 MeV Signal from Cl-36, as a Function of Chlorine Amount, Alongside Background Signal at Outside Surface of Concrete Overpack.

Figure 8. 6.11 MeV Gamma Counts vs. Amount of Chloride.

Figure 9. 7.41 MeV Gamma Counts vs. Amount of Chloride.

Reducing Risks in Nuclear Power Plants Operation by using FeCrAl Alloys as Fuel Cladding

Figure 1. Risk management environment model for a nuclear power plant operator.

Figure 2. Five metric Areas Provided by DOE to Evaluate ATF.

Figure 3. Part 1, Plan view of Zircaloy-2 and APMT coupons exposed to BWR simulated conditions for one year (288°C + 2 ppm O

2

)[10].

Figure 3. Part 2, Cross sections of Zircaloy-2 and APMT coupons exposed to BWR simulated conditions for one year (288°C + 2 ppm O

2

)[10].

Figure 4. Cross sections of APMT coupon exposed to PWR simulated conditions for one year (330°C + 3.75 ppm H2). The average oxide thickness is 87 nm[10].

Figure 5. Mechanical properties and elongation to failure of Zircaloy-2 (longitudinal) and APMT without irradiation (at the beginning of life, no irradiation).

Figure 6. Parabolic rate constant of several engineering alloys in 100% superheated steam[16].

Annular Accident Tolerant Fuel with Discs and Rod Inserts

Figure 1. Exploded View of Annular Fuel with Discs and Rod Inserts.

Figure 2. Variation of Peak Temperatures with Linear Heating Rate for Select Configurations.

Nanocarbon-Infused Metals: A New Class of Covetic Materials for 207 Energy Applications

Figure 1. Effect of impurity concentrations of selected elements on conductivity of copper[12], [Source: “High Conductivity Copper for Electrical Engineering,” Copper Development Association (CDA) Publication 122, 2016.]

Figure 2. XRD pattemsof(a)parentcopperCuPaand (b) covetic copper CuCv

3

.

Figure 3. Fracture surface SEM micrograph of CuPa (a, b) and CuCv

3

(c, d) at different magnifications.

Figure 4. Differential scanning calorimetry spectrum of CuPa and CuCv

3

in flowing nitrogen atmosphere.

Figure 5. Voltage vs. current curves of (a) CuPa and (b) CuCv

3

samples measured by four-probe method.

Figure 6. Temperature-dependent thermal conductivity of CuPa and CuCv

3

samples measured by the flash method (ASTM E1461-13).

The Study of Catalysts Based on Intermetallic NiAl Alloys

Figure 1. Structure of NiAl SHS-catalyst

Figure 2. The catalytic activity of the catalysts studied in oxidation reactions

Figure 3. Catalytic activity of the investigated catalysts depending on the volumetrical consumption of the reaction gases mixture in oxidation reactions at 450 °C temperature

Guide

Cover

Table of Contents

Green and Sustainable Technologies for Materials Manufacturing and Processing

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Preface

This volume contains 20 papers presented during the Materials Science & Technology 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:

8th International Symposium on Green and Sustainable Technologies for Materials Manufacturing and Processing

Construction and Building Materials for a Better Environment Materials Issues in Nuclear Waste Management in the 21st Century

Materials Development for Nuclear Applications and Extreme Environments Nanotechnology for Energy, Healthcare, and Industry

Materials and Processes for CO

2

Capture, Conversion, and Sequestration

The success of these symposia and the publication of the proceedings could not have been possible without the support of The American Ceramic Society and other organizers of the program. The program organizers and session chairs for the above symposia are appreciated. Their assistance, along with that of the reviewers was invaluable in ensuring the creation of this volume.

TATSUKI OHJI, AIST, JAPAN

JOSEF MATYÁŠ, Pacific Northwest National Laboratory, USA

HENRY COLORADO, Universidad de Antioquia, Colombia

RAGHUNATH KANAKALA, University of Idaho, USA

Green and Sustainable Technologies for Materials Manufacturing and Processing

TITANIA NANOSHEET PRODUCTION BY AN INEXPENSIVE GREEN PROCESS

Cody Cannon and Allen W. Apblett

Oklahoma State University

Stillwater, OK, USA

ABSTRACT

Anatase nanosheets were synthesized via a facile green process that involved isothermal aging of a titanyl sulfate solution at 60 °C. The process produced two distinct titanium products a stable colloid composed of anatase nanosheets that were on average 1.53 nm or approximately 4 unit cells in height. Due to a preferential growth axis the nanosheets imaged by TEM displayed the (101) face of anatase. The colloids had a markedly high band gap of 3.82 eV, which is higher than typical for nanoparticles of similar dimensions and was only reported in one other synthesis for nanosheets. This increase in the band gap can be contributed to the 2D quantum confinement of the nanosheets. The precipitated solid was also characterized and determined to be anatase nanosheets. The nanosheets in the precipitates were found to be on average 3.93 nm in thickness. This equates to roughly 11 unit cells on average. The precipitates tended to form aggregates that were on average 96.9 nm in diameter as measured by AFM. The sheets in both cases were found to have a preferential growth axis and the lattice fringes of the (101) anatase planes were very evident in the TEM images of both materials. The aggregated anatase nanosheets were found to be photocatalytic and were able to oxidize methylene blue. Titanium nanosheets with (101) exposed faces are of particular interest for many applications including dielectrics, photovoltaics, and photocatalysis due to the many exposed defects on the surface giving rise to unique properties.

INTRODUCTION

The discovery of the photocatalytic splitting of water by Fujishima and Honda using titanium dioxide and ultraviolet light has encouraged a large amount of research in TiO21. Titanium (IV) oxide has been shown to be extremely versatile and has many applications in areas such as photocatalysis1, UV filters,2–3 water purification4–5 and solar cells6–8 to name a few. In the past few years a new push in titanium research has focused on methods for the preparation and applications of nanosized titanium particles9–11. These nanoparticles are of great interest due to their potential to have unique properties in comparison to the bulk materials that will meet the needs for a wide variety of applications.

The increase in surface area of nanomaterials as the surface to volume ratio increases with decreasing particle size often results in increased reactivity due to an increase in surface active sites. Anatase nanoparticles are of particular interest because their photocatalytic properties are superior to the other two phases of TiO2, brookite and rutle12. echniques including sol-gel13–14, hydrothermal methods15, and gas condensation16. The hydrothermal method utilizes titanium salts that undergo hydrolysis under specific conditions to form titanium dioxide and is one of the most robust and tunable methods. There are many methods used for the hydrothermal production of photoactive titanium oxide. Bavykin et al. used a seeded titanium sulfate solution with reflux and various acid types to investigate the impact on morphology17. The author observed that hydrolysis occurred slowly at 70 °C under reflux conditions and that anatase phase particles only formed after prolonged reflux. It was also shown that a wide variety of titanium materials with different particle sizes can be tailor made by just fine tuning the acid concentrations or by the addition of a second mineral acid. Seishiro et al. were able to produce anatase phase titanium using ethanol and titanium sulfate under reflux via hydrolysis resulting in the synthesis of anatase TiO218. There are many other hydrothermal synthesis that produce photoactive anatase titanium but all involve refluxing or the use of an organic templating agent or seed nuclei, or high temperature calcining in order to produce the anatase phase product.

In this investigation a low temperature isothermal method was applied to an aqueous titanium sulfate solution in order to produce two separate nanometric titanium products. The first of these is a nanocrystalline anatase titanium dioxide aggregate that has photocatalytic properties. This synthesis also results in the preparation of a stable aqueous titanium dioxide colloidal suspension. This colloid consists of anatase phase nanosheets that are stable for more than six months of storage.

EXPERIMENTAL

Materials and Methods

The titanium sulfate used was obtained from Alfa-Aesar and all other chemical reagents used in the experiments were all obtained from commercial sources with ACS-grade purities and were used without further purification. Water was purified by reverse osmosis followed by deionization. X-ray powder diffraction (XRD) was performed using a Bruker D8 powder diffractometer in order to analyze the structural properties of the synthesized titanium powder. Morphological features of the powder samples and colloid were determined using transmission electron microscopy (JOEL JEM-2100). The solid sample was embedded and sectioned in order to image the sample by transmission electron microscopy while a drop of the colloid solution was allowed to evaporate on a TEM grid and then imaged. BET nitrogen adsorption measurements were made using a Quantacrome Nova 1200 to determine the surface area of the synthesized titanium dioxide nanoparticles. Atomic force microscopy was used in tapping mode to determine the height of the colloid particles and the precipitate. Both samples were placed on a clean piece of mica by placing a drop on the surface and allowing it to evaporate. The precipitate was suspended and allowed to settle prior to placing the drop on the mica. Raman and IR spectra were collected for the synthesized nanoparticles using a Nicolet NXR 9610 FT-Raman spectrometer with a fixed laser of 976 nm and a Nicolet 750 FT-IR instrument. The FTIR spectra were collected by grinding the precipitated samples with KBr and pressing the sample into a transparent pellet that was then run in transmittance mode on the FT-IR. Particle size analysis of the colloid and an aqueous suspension of the prepared nanoparticles was performed using a Malvern HPP5001 dynamic light scattering instrument. UV-Visible spectra of the suspended nanoparticles and the colloid were recorded using a Cary 100 UV-Visible spectrometer.

Synthesis of Titania Nanosheets

A titanyl sulfate solution (0.2 M) was prepared in an Erlenmeyer flask by adding 12.01 g (.083 moles) of titanium oxide sulfate sulfuric acid hydrate to 200 mL of deionized water. A half of a molar equivalent of concentrated sulfuric acid (4.28 g) was then added (4.18 g) and the solution was carefully heated with stirring. As the titanyl sulfate dissolved the white color faded and the solution turned transparent. As soon as this occurred, the flask was removed from the heat and allowed to cool to room temperature. It was then placed in a screw cap glass bottle and heated at 60 °C for 72 hours. During this time, a white precipitate formed that was isolated by centrifugation at 3000 RPM for 1 hour. The supernatant was a colloidal suspension that was poured off and saved. The solid was then washed three additional times with 200 mL aliquots of deionized water by a resuspending/centrifugation process. The suspension was stored in a glass bottle while the solid was vacuum dried at 1 atm until a constant weight was achieved. After drying 1.72 g of the titanium precipitate product was obtained corresponding to a 26 percent yield based on the hypothesis that all of the available titanium in the solution was precipitated as titanium dioxide. Assuming that the remaining titanium is in solution as the colloid, approximately 74 percent (4.9g) of the titanium dioxide is present in the colloid. This would give the colloid a concentration of 0.31 M. The titanium content determined gravimetrically was 85% corresponding to 1.46g of titanium dioxide.

RESULTS AND DISCUSSION

X-ray powder diffraction demonstrated that the titanium dioxide precipitate that was formed was composed exclusively of nanocrystalline anatase phase of titanium dioxide. This is illustrated by the excellent match to the ICCD powder diffraction file (# 03-065-5714) and the absence of any characteristic peaks of rutile or brookite phases at 27° and 31° respectively in the pattern (Figure 1). The broadening of the XRD peaks is characteristic of a nanocrystalline material, indicating that the material is an aggregate of nanocrystalline anatase titanium that has some long-range order since XRD gives an average of the order over several unit cells. The Scherrer equation. used to calculate the crystallite size of the titanium aggregates using the (101) peak, indicated that the lower boundary on the particle size was 11.2 nm.

Figure 1. X-Ray Powder Diffraction Pattern of Titanium Nanosheet Precipitate with the ICDD Diffraction Pattern File for Anatase in Grey.

Transmission electron microscopy was used to determine the morphology of the materials. The colloid material was diluted 1000 fold and then drop cast onto a copper TEM grid and allowed to air dry. The TEM micrographs showed that the particles aggregated during the drying process (Figure 2A). The nanoparticles have no discernable uniform shape but they do appear to have very flat surfaces and they also have very low contrast with the grid. These facts suggest that the colloid is composed of nanosheets of titanium dioxide. The particles range in size from 4.0 nm to 7.0 nm in diameter. The lattice fringes of the titanium colloid are visible in Figure 2B. When the particles are measured from fringe edge to fringe edge they are also found to range in size from 4.0 to 7.0 nm. The lattice fringes occupy the entire volume of the particles indicating they are single crystals. Image J software was used to measure the spacing between lattice fringes of a number of particles in the image. These were all found to have the same spacing of 3.5 Å that corresponds to the (101) face of anatase. This face is a step edge that is composed of monoatomic height steps and is the most commonly observed crystal face in anatase titanium dioxide19. The (101) surface is of great interest because of the potential photocatalytic and solar cell applications of TiO220–21.

The precipitated titanium dioxide was prepared for electron microscopy by suspending the particles in deionized water and sonicating for one hour. The suspension was then drop cast onto a copper TEM grid and the water was allowed to evaporate (Figure 2C). These particles are much larger in size than the colloid particles and are also aggregated. The crystallites were flat and the lattice fringes could easily be observed and made up the entire volume of the observed particles. Like the colloid the particles appeared to be flat and gave low contrast indicating that the aggregates were composed of thin nanosheets. The suspended particles had a crystallite size ranging from 10 nm to 35 nm and formed aggregates that are between 100 to 300 nm in diameter. The spacing of the lattice fringes was 3.5 Å corresponding to the 101 planes of anatase.

In order to determine if the aggregation seen in the micrographs was due to the technique used in preparing the samples for TEM or if it was occurring in solution the precipitated sample was also embedded in resin, (Figure 2D) sectioned with a microtome, and then imaged. TEM micrographs of the sections material showed aggregated crystallites that matched those observed in the suspended samples in both size and morphology. This confirms that aggregation occurred during the precipitation process and was not an artifact of TEM sample preparation.

The results from the TEM and XRD characterization indicate that during the static 60 °C heating process the formation of anatase phase titanium nanosheets takes place. Through centrifugation it was possible to separate the aggregates from the suspended nanosheets of titanium dioxide resulting in isolation of both a stable colloidal suspension of anatase nanosheets and a nanocrystalline aggregate of anatase nanosheets. The phase of both the products was confirmed through d spacing measurements in the TEM and the powder X-ray diffraction pattern of the precipitated solid. The phase identification for the colloid is based on the d spacing measurements of the TEM only.

From the TEM and XRD results a hypothesis can be made concerning the process of the formation of the particles. When the solution is isothermally heated at 60°C the nucleation of nanometric titanium dioxide particles begins slowly over time resulting in the formation of anatase nanosheets. Once these particles grow and reach about 10 nm in diameter they began to aggregate and form nanocrystalline solids that precipitate out of solution. This is supported by both the TEM and XRD results since all of the observed particles in the colloid by TEM were measured to be less than 10 nm in diameter. From the XRD we can use the Scherrer equation to determine the lower limit of the crystallite size of the sample by measuring the full width of the peak at half height. The titanium precipitate gave a lower boundary of 11.2 nm, further supporting the idea that the sheets are aggregating once they reach about 11 nm in diameter. If this were not the case we would have expected a much smaller value for the Scherrer calculation since particles of a smaller diameter were readily available in solution to be incorporated into the precipitates. From the TEM results, it can be estimated that the aggregates have crystallite size ranging from 10 to 35 nm. This indicates that the particles still grow once they have fallen out of solution and aggregated leading to many crystallites larger than 10 nm in diameter in the precipitated nanosheet aggregates.

Figure 2. TEM images of (A) titanium colloid nanosheets, (B) titanium colloid nanosheets with visible lattice fringes, (C) precipitated titanium nanosheets with visible lattice fringes, and (D) precipitated titanium nanosheets embedded and sectioned

Atomic force microscopy (AFM) was used in order to confirm that the findings of the TEM images that the particles were nanosheets. The AFM images were obtained in tapping mode and the height, width, and length of the particles were determined. The colloid sample aggregated when being placed on the mica causing the diameter measurements to not be usable but the height of the nanosheets could still be determined. The software was set to measure the height from the mica to the surface of the titanium nanosheets. Figure 3 shows the height of the nanosheets from the colloid samples based on the height measurements. The mean height of the colloid sample from 82 measurements was found to be 1.53 nm with a maximum of 3.22 nm and a minimum of 0.37 nm. The AFM image of the precipitated particles is shown in Figure 4. From this data it was possible to measure both the heights and diameters of the precipitated particles. The height based on 52 measurements was found to have a mean of 3.93 nm with a minimum of 1.28 nm and a maximum of 5.74 nm. The diameter was also based on 52 measurements and was found to be 96 nm with a minimum of 55 nm and a maximum of 182 nm.

Figure 3. (A) Distribution of Height Measurements of (A) Titanium Colloid Nanosheets (B) Precipitated Titanium Nanosheets (C) Distribution of Diameter Measurements of Precipitated Titanium Nanosheets

Figure 4. Atomic Force Microscopy Images of Titanium Colloid Nanosheets (Left) and Precipitated Titanium Nanosheets (Right)

Since the particle size measurements from both the AFM and the TEM are in agreement it can be concluded that the titanium particles are orienting the same way on the mica as they do on the TEM grid. This allows use of the unit cell dimensions of anatase to determine how many units thick the nanosheets are. Due to the fact that the particles have the (101) face oriented upward and that anatase has a tetrahedral unit cell it can be concluded that the (101) planes would run perpendicular to the imaged face and along the horizontal axis of the nanosheets. Using the lattice parameters for anatase the corresponding d-spacing was calculated to be 0.351 nm. By dividing the mean height of the nanosheets as measured by AFM it was possible to estimate the height of the nanosheets in unit cells. The AFM measurements for the colloid indicate that the sheets are on average 4 unit cells tall with some measuring as small as 1 unit cell and others as tall as 9 unit cells. The precipitated sheets were found to be slightly thicker with an average thickness of 11 unit cells, a minimum of 4 unit cells and a maximum of 16 unit cells. These measurements combined with the TEM data indicate that aging the titanyl sulfate solution at 60 °C produced anatase nanosheets. These sheets are severely truncated in one crystallographic direction and this might lead to interesting and unique properties.

Raman spectroscopy is very sensitive to the crystallinity and microstructure of a sample. Due to the fact that Raman peaks become very broad and shrink in intensity when local imperfections exist Raman spectroscopy can be used as a good indicator for crystallinity in samples of anatase. The Raman spectrum of the precipitated material (Figure 5) had characteristic peaks for crystalline anatase at 157, 399, 519, and 639 cm−1 and matched that reported by Zhang et al. The three higher frequency peaks are well resolved indicating the nanocrystals have good crystallinity with few defects22–23. The broadening that is observed in the spectrum and the shift in the Eg(1) peak at 157 cm−1 from 151 cm−1 in the precipitated anatase is an indication of nanocrystalline anatase. By comparing the peak shift from our results to that of literature values gathered by Swamy et al. shifts for nanocrystalline anatase in the Eg1 peak to 157 cm−1 is indicative of samples that are around 5 nm in diameter. The full width at half maximum measurement of this peak was found to be 32 cm−1 and is also consistent with a particle diameter of 5 nm. This is in agreement with the XRD and AFM measurements and supports the presence of anatase.

Figure 5: Raman Spectrum of Precipitated Anatase Phase Titanium Nanosheets

The infrared spectrum of the titanium dioxide precipitate was measured (Figure 5.7) and was compared to literature values.24–25 The spectrum has a broad peak from 3100-3500 cm−1 that corresponds to O-H stretching of either free or bound hydroxyl groups. This is also shown by the small peak at 1630 cm−1