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TRANSCRIPT
HIGH PRESSURE STUDY OF SPINEL CHROMITE
by
ALLEN D.C. WHITE, B.S.M.E.
A THESIS
IN
MECHANICAL ENGINEERING
Submitted to the Graduate Faculty of Texas Tech University in
Partial Fulfillment of the Requirements for
the Degree of
MASTER OF SCIENCE
IN
MECHANICAL ENGINEERING
Approved
Yanzhang Ma Chairperson of the Committee
Atila Ertas
Valery Ilich Levitas
Accepted
John Borrelli Dean of the Graduate School
May, 2005
ii
ACKNOWLEDGMENTS
First and foremost, I would like to thank my advisor Dr. Yanzhang Ma for his
guidance, motivation, and most importantly the many hours spent in both New York and
Lubbock making this paper possible. Thank you also to Dr. Atila Ertas and Dr. Valery
Levitas for being cooperative committee members throughout this study. I would also
like to thank Resul Aksoy, Emre Selvi, and Jagdev-Singh Sandhu for their assistance in
the experiments and data processing, and also the numerous discussions in the lab. Other
thanks go to Dr. Guo, Dr. Hu, and Mr. L.A. Reis for helping out in different phases of the
study, and to the College of Engineering and the Mechanical Engineering department for
financial support of this project.
Other than academic assistance, I would like to thank my family and friends for
their love and support throughout my life, there are no words to describe my gratitude to
them and everything they have done.
iii
TABLE OF CONTENTS
ACKNOWLEDGEMENTS……………………………………………………….………ii
ABSTRACT………………………………………………………………………….…....v
LIST OF TABLES…………………………………………………………………….….vi
LIST OF FIGURES…………...........................................................................................vii
CHAPTER
I. INTRODUCTION…………………………………………….……………...…1
1.1 The Spinel Structure……………………………………………..…………..1
1.2 Chromites…………………………………………………………….....……3
II. EXPERIMENTAL METHODOLOGY………………………………….....….6
2.1 Diamond Anvil Cell…………………………………………………...…….6
2.2 Energy Dispersive X-ray Diffraction……………………………………..…8
2.3 Ruby Fluorescence, a Pressure Sensor…..………………………….……...11
III. EXPERIMENTAL SETUP…………………………………………………..14
3.1 Sample Characteristics…………………………………………………….14
3.2 Diamond Anvil Cell…………………………………………………...…..14
3.3 Gasket Preparation……………………………………………………...…15
3.4 Sample Loading………………………………………………………..….19
3.5 Pressure Medium………………………………………………...…….….21
3.6 Pressure Measurement…………………………………………...……......24
3.7 Energy Dispersive X-ray Diffraction Measurements……………………..25
iv
IV. RESULTS AND DISCUSSION………………..…………………………....29
4.1 Results and Discussion...…………………………………………….........29
4.1.1 Lattice Change of Chromite under Pressure………………….........29
4.1.2 Equation of State of the Spinel Chromite and Pressure Medium…………………………………………………………….33 4.1.3 Pressure Induced Phase Transformation of Chromite…...………...35
4.2 Conclusion...……………………………………..…………………….….37
REFERENCES………………………………………………………………………..…39
APPENDIX…………………………………..………………………….……………….44
v
ABSTRACT
Chromite has one of the most important crystal structures, the spinel structure;
therefore its high pressure behavior has significant implications to the foundation of a
wide range of materials. It is also found throughout our Earth’s interior. These facts
make its high pressure studies important to materials science, physics, geosciences, and
crystallography. Synchrotron X-ray diffraction measurements of chromite were
performed using a symmetrical diamond anvil cell to 41.2 GPa. The data was fit using
the third order Birch-Murnaghan equation of state, and the bulk modulus KOT was
determined to be 197±19 GPa with K′OT=66±12 when fitting data to 16 GPa. Further
investigation revealed a pressure induced phase transformation at 28.2 GPa.
vi
LIST OF TABLES
2.1 Culet diameters…………………………….……………………………………..…...7
3.1 Indentation pressures……………………………………………….………………..17
3.2 Pressure media and their hydrostatic limits……………………………………….…22
4.1 Refinement results……………………………...…….………………………...……32
vii
LIST OF FIGURES
1.1 The spinel structure………………………..……………………………………..……2
1.2 The chromite structure……………………………….…………………………..……4
2.1 Diamond anvil cell; (a) disassembled; (b) assembled……………………………...….8
2.2 An X-ray diffraction pattern from an EDXRD experiment……………….……..……9
2.3 Ruby fluorescence measurement system……………..……………………………...12
2.4 Ruby spectrum under hydrostatic conditions………...……………………………....12
3.1 Unaligned and aligned DAC…………………………………………………………15
3.2 Deformation of gasket under pressure; (a) below 5 GPa; (b) above 5 GPa……….…16
3.3 Electronic drilling machine……………..……………………………………………18
3.4 Gasket; (a) before indentation; (b) after indentation; (c) with machined sample chamber……………....................................………….…19
3.5 Schematic of loaded DAC……………….…………………………………………..20
3.6 Picture of sample and ruby loaded in the gasket……….………………………….…21
3.7 Pressure medium loading apparatus……...………………………..……...……….…24
3.8 Observed ruby spectrum at 41.2 GPa……………………….……….………………25
3.9 EDXRD system……………………………….………………………………...……26
3.10 X-ray beam intensity distribution………….………………………………….....…27
3.11 Transmitted and diffracted X-ray with 2θ angle………..………………………..…28
4.1 X-ray diffraction pattern at 3.5 GPa………….……...…………………...………….30
4.2 X-ray diffraction patterns at different pressures…...……..……………………….…31
4.3 Effect of pressure on the d-spacings of spinel chromite…………….……………….31
viii
4.4 Cell parameter reduction with pressure………….…...……………………………...32
4.5 Equation of state of chromite………………………….……………………………..34
4.6 Equation of state of argon with measured volume at pressures…………..…………35
4.7 Comparison of the X-ray diffraction pattern before and after the phase transformation………..…………………………………………………..….36
4.8 d-spacings as a function of pressure, emphasizing the structural change at 28.2 GPa and above…………………..…………………………………37
1
CHAPTER I
INTRODUCTION
1.1 The Spinel Structure
A spinel material is a molecular compound with the AB2O4 formula. With the A
and B being metal ions with valences of 2+ and 3+, respectively, spinel compounds are
known to crystallize into a cubic structure with the space group Fd3m [1, 2]. There are
two types of spinel structures at ambient conditions, the normal (AB2O4) and inverse
(B2AO4) spinel. In the ideal normal spinel, A and B ions occupy the tetrahedral (T) and
octahedral (M) sites, respectively; in the inverse spinel, half of the B ions center the
fourfold coordination, with the consequent migration of all the A ions to the octahedral
sites [3, 4]. A full description of spinel structure geometry includes a cell edge, a
tetrahedral unshared edge, an octahedral unshared edge, an octahedral edge shared with
other octahedra, T-O and M-O bond distances, and an octahedral O-M-O angle [5]. An
illustration of this structure is shown in Figure 1.1 [6]. The blue spheres are oxygen
atoms, and the green and red spheres are the A and B ions, respectively.
Spinel materials are binary oxides, which occur in numerous industrial processes
and have important technological applications. Petric and Jacob reported that spinels are
formed as stable corrosion products when alloys are exposed to an oxidizing atmosphere
[7]. As such, they are beneficial in providing a protective layer between the alloy and
gas, inhibiting further corrosion. Also, fused cast spinel-type refractories show superior
erosion resistance to molten coal slag and are expected to find applications in coal
2
gasification systems [7]. In addition, owing to favorable electrical properties, certain
spinels have been considered as candidate materials for magneto hydrodynamic
electrodes and as a promising material (in particular, LiMn2O4) as a cathode for Lithium
batteries [8]. Other areas in which spinels are used are as a catalyst for the
decomposition of chlorinated organic pollutants [9], as magnetic materials [10],
superhard materials [11], high temperature ceramics [12], as well as high pressure sensors
[13]. This extensive class of structures also exists in significant abundance in the Earth’s
interior [(Mg, Fe)2SiO4 are the most common minerals in the Earth’s upper mantle [14]]
and plays an important role in determining the physical properties our planet. Due to
their importance in materials science, physics, geosciences, and crystallography; spinel
compounds have been extensively explored.
Figure 1.1. The spinel structure. The red cubes are also contained in the back half of the unit cell [6]
3
Studies have also been conducted to investigate the pressure induced phase
transformations of spinel-type structures [3, 15-19]. Results reveal two types of high
pressure behaviors: one undergoes a pressure induced phase transformation from the
spinel structure to its high pressure polymorph [3, 15, 18, 19]; and the other dissociates to
a mixture of its constituent oxides [16]. Although the spinel structure has been
extensively studied, previous high pressure investigations only focused on particular
spinels based on their geophysical significance, mostly relevant to the constituents of the
Earth’s interior, including Fe, Mg, Al, Si, and Ge [15,18,19,20]. With these scarce data,
it is hard to obtain a complete understanding of the high pressure behavior of spinels [5].
Other studies include determining equations of state for numerous spinels [21-23] as well
as theoretical calculations with the goal of describing this wide array of structures.
1.2 Chromites
Chromites, which are molecular compounds with the ACr2O4 formula, have a
normal type spinel structure [24,25], i.e., the tetrahedra of oxygen atoms surround
divalent metal ions and the octahedra of oxygen surround chromium ions [26]. An
illustration of a chromite structure is shown in Figure1.2 [6]. It should be noted that the
structure is identical to Figure 1.1, except the red spheres are chromium ions. Chromites
are considered as a significant spinel system with numerous potential applications. One
particular chromite, iron chromite (FeCr2O4), is known to occur due to different industrial
processes. It has been confirmed that FeCr2O4 can form in abundance on the surface of
stainless steels during welding, and also upon oxidation in air when stainless steel pipes
4
are exposed to high temperature steam in power plants [27]. Other reports indicate that
FeCr2O4 can be created on the surface of metals by bringing a mixture of Cr2O3 and Fe
powder in contact with a high energy laser, producing a coating on the parent metal to
meet extreme conditions of wear and corrosion resistance [28].
Chromites also occur naturally in our Earth, and are used for the production of
ferrochrome (important alloying agent in stainless steel making) [29], metallic chromium,
chromium chemicals, and refractories [30]. Another reason why chromite is important
was reported by Griffin and Ryan, stating that the evidence of chromites in the Earth’s
interior can be used in conjunction with certain methods (see reference for more details)
in order to target certain regions for diamond exploration [31].
Figure 1.2. The chromite structure. The red cubes are also
contained in the back half of the unit cell [6]
5
Although chromites are widely used, very few studies have been performed on
this structure. The first natural sample of iron chromite with the calcium ferrite (CF)
structure, which was found in the shock veins of the Suizhou meteorite, was reported by
Chen et al. [32]. They also discovered that iron chromite spinel transforms to the CF
structure at 12.5 GPa and to the calcium titanite (CT) structure above 20 GPa. The
experimentally calibrated CF and CT polymorphs of chromite could therefore be an ideal
pressure gauge not only for shock-metamorphosed terrestrial rocks and meteorites but
also for mantle rocks covering the important pressure range throughout the transition
zone [32]. Other investigations include ZnCr2O4 and MgCr2O4 chromites, where a
pressure induced phase transformation from the spinel structure to a high pressure
polymorph was observed [33, 34]. On the contrary, one ab initio calculation has been
performed to investigate the phase transformation of the chromites [16], and the
simulation predicts that they dissociate to their constituent oxides at high pressure and
room temperature, which disagree with experimental results. Due to these disagreements,
a systematical high pressure experimental study of a spinel chromite is critical to clarify
the contradiction as well as providing information that can lead to a better understanding
of the group of compounds that crystallize in spinels and similar structures.
6
CHAPTER II
EXPERIMENTAL METHODOLOGY
2.1 Diamond Anvil Cell
The diamond anvil cell (DAC) is fast becoming the most powerful ultra-high
pressure device; permitting engineers, materials scientists, physicists and chemists to
discover new states of matter and understand the physics and chemistry underlying
ultra-high pressure phenomena. The basic principle of the DAC is very simple. A sample
placed between the parallel faces of two opposed diamond anvils is subjected to
compression when opposite forces push the two opposed anvils together [35]. Since
pressure is defined as force divided by area, it is possible to reach higher pressures either
by increasing force or decreasing area. If one wishes to achieve high pressures by
decreasing area, then they must be willing to study small samples [36]. The small size of
the sample, and hence, of the anvils, reduces the requirements for large forces and large
supporting frames. The small anvil size has the additional advantage that it permits the
selection of a rather exotic material with just the right properties to be investigated. Also,
the cost of such a device is quite modest when compared with other high pressure devices
[36]. Today a DAC capable of generating pressures greater than 100 GPa can fit into the
palm of the hand and a number of sophisticated measurements, including X-ray
diffraction and a variety of spectroscopies, can be performed on materials of microscopic
dimensions [35].
7
The frame of the DAC is made of stainless steel and the supporting seats
(platens) are usually made of tungsten carbide, both of which have openings along the
axial direction in order for measurements to be performed on the sample. The anvils are
usually made of diamond, which is the hardest substance known to man and is quite
transparent to X-rays and light making it the ideal material [35]. They are usually
selected from brilliant-cut gem stones, are ground and polished into the desired shape
(8 or 16 edges) and size, depending on the pressures that are required to be achieved in a
given experiment. A list of several different flat culet diameters and their respective
pressures that can be obtained is shown in Table 2.1 [37]. A picture of a typical
symmetric DAC is shown in Figure 2.1.
Table 2.1. Culet diameters [37]
Culet dia. (µm) Highest pressure (GPa)
500 ~60
400 ~70
300 ~70-80
200 ~90
100 ~100-150
8
(a) (b)
Figure 2.1. Diamond anvil cell; (a) disassembled; (b) assembled
2.2 Energy Dispersive X-ray Diffraction
Energy dispersive X-ray diffraction (EDXRD) is a non-destructive materials
characterization technique that has been used for many years in numerous fields ranging
from engineering to biology. Buras et al. [38] were the first to use EDXRD techniques
with the DAC interfaced to synchrotron radiation. Since then synchrotron X-ray
diffraction has become a well-established technique and has long been successfully
applied in high pressure and high temperature studies in the diamond anvil cell [39], with
numerous synchrotron facilities worldwide allowing many scientists accessibility to
conduct experiments.
With synchrotron radiation, electrons or positrons are set into motion, orbiting
around a storage ring and emitting electromagnetic radiation. This radiation results from
the centripetal acceleration of the electrons by the magnetic fields in the storage ring.
High energy X-rays are produced, which can be useful for X-ray diffraction on a variety
of samples [14].
9
When performing structural determinations using a DAC, a germanium
charge-coupled device (CCD) detector is usually used for collecting the diffracted
X-rays; due to their stopping power in the 15-100 keV range which is generally the range
used by DAC users [40]. Combined with certain software, the data is displayed in
graphical form. A typical graph from an EDXRD experiment using a DAC is shown in
Figure 2.2.
10 20 30 40 50 60 70
0
1000
2000
3000
4000
Inte
nsity
(co
unts
)
Energy (keV)
Figure 2.2. An X-ray diffraction pattern from an EDXRD experiment.
Included in the graph are fluorescences of some materials.
10
When performing EDXRD for determining structures, the lattice parameters (a, b,
c, and α, β, γ) are determined through measurements of lattice spacings hkld ( h , k , l are
Miller indices) and the atom positions within the crystalline unit cell, which are derived
from the energy values of the centers of intense peaks seen in the data [41], similar to
Figure 2.2. The analysis uses Bragg’s law [42], which gives a relationship between the
interplanar lattice spacings hkld , reinforced diffracted beams of wavelength λ , and
pre-determined EDXRD angle Θ2 . It is shown in the following Equation,
Θ= sin2 hkldλ . (2.1)
Then using the relationship of the wavelength-frequency exchange, which can be
expressed as
υ
λc
= (2.2)
where c is the speed of light and υ is the frequency of the light, as well as
υhE = (2.3)
where E is the photon energy of the X-ray and h is Planck’s constant; with simple
manipulation the final form of
Θ
=Θ
=sin
Å1993.6sin2
keVhcEd (2.4)
is produced. This equation shows that if Θ2 is held constant (which is the case in
EDXRD), Ed becomes a constant. This allows one to determine lattice spacings from a
diffraction pattern similar to Figure 2.2.
11
High pressure phase identification using synchrotron EDXRD techniques involves
many advanced experimental methods, so error evaluation becomes a most important
issue [43]. One possible source of error arises when using Bragg’s law (Equation 2.1),
which shows the necessity of carefully determining the diffraction angle 2Θ in order to
obtain accurate results. Another possible source of error in a high pressure EDXRD
experiment is the significant heating of the DAC which can cause a slight shift in the
lattice parameter. This occurs due to the diamond anvils and sample absorbing much of
the X-rays with energies less than 10 keV [44].
2.3 Ruby Fluorescence, a Pressure Sensor
The use of the wavelength shift of the ruby R1 fluorescence line to determine
pressure was originally developed by Forman, Piermarini, Barnett and Block [45].
The original calibration of this method involved observing the shift with pressure of the
ruby R1 line, while simultaneously measuring the specific volumes of several metals (Cu,
Mo, Pd, and Ag) by X-ray diffraction. The absolute pressure was obtained indirectly by
making reference to the isothermal equations of state of the metals derived from
shock-wave data [46]. After being revised numerous times, the ruby fluorescence
method has been widely used throughout the world as the common pressure scale for
high pressures above 10 kbar (1 GPa).
When used in a DAC, a ruby chip is placed in the sample chamber along with the
pressure medium and sample, and the fluorescence is excited by a laser or any strong
light source. An optical detector collects the signal and it is then displayed as a graph
12
showing intensity versus wavelength. A typical setup of a system with a corresponding
graph are shown in Figures 2.3 and 2.4, respectively. The R lines of ruby are quite
intense, and under hydrostatic pressure they shift linearly to higher wavelengths [35].
Figure 2.3. Ruby fluorescence measurement system
702.5 705.0 707.5 710.0 712.5300
400
500
600
700
800
900
R2 Line
R1 Line
Inte
nsity
Wavelength (nm)
Figure 2.4. Ruby spectrum under hydrostatic conditions
13
Measurement of the wavelength is commonly obtained by determining the
wavelength, λ , of the maximum intensity of the R1 line [47]. This value is then used in
conjunction with
−
−+= 11
1904
0
0
B
BP
λ
λλ (2.5)
to determine the pressure inside the sample chamber, where B is the curvature parameter
(7.665 for hydrostatic, 5 for quasi-hydrostatic), λ is the measured wavelength, and 0λ is
the wavelength of the maximum intensity of the R1 line at ambient pressure (694.24nm).
Although the ruby fluorescence scale is accurate under hydrostatic conditions,
when hydrostaticity diminishes it introduces larger error. When ruby is subjected to
non-hydrostatic stress, the R lines become broader. Pure uniaxial stress gives an even
greater broadening effect than non-hydrostaticity. This feature of increasing line width
makes ruby a useful sensor for detecting the limits of hydrostaticity under pressure [47].
14
CHAPTER III
EXPERIMENTAL
3.1 Sample Characteristics
The sample, (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4, is a type of chromite which is dark
reddish brown in color and has the cubic fcc spinel structure (space group Fd3m) at
ambient conditions (see Figure 1.2) [48]. The sample is a natural mineral which
originated from the Philippines and whose composition is made up of FeO(12.27wt%),
MgO(15.85wt%), Cr2O3(64.77wt%), and Al2O3(7.23wt%); yielding the
(Fe0.44Mg0.56)(Cr0.89Al0.11)2O4 compound [49].
3.2 Diamond Anvil Cell
A symmetrical DAC with 300 µm flat culet diamonds was used in the experiment.
A picture of the DAC is shown in Figure 2.1. Before using the DAC in the experiment,
the culets were aligned to the rotational center of the cell as to eliminate any stress
concentrations which could cause the diamonds to crack under high pressure. This was
achieved by first tightening the set screws to a point where the diamonds could not come
in direct contact with each other. Next, the diamonds were aligned using the lateral
translation screws. The cylinder was then held stationary and the piston was rotated 180°.
After rotation, the diamond mounted in the piston was checked for alignment with the
cylinder diamond and, if misaligned, was translated halfway to the position of the center
of the stationary cylinder diamond via the lateral translation screws. The cell was then
15
flipped over and the cylinder diamond was aligned with the diamond in the piston. The
piston was held stationary while the cylinder was rotated 180° and, if misaligned, the
cylinder diamond was translated halfway to the center of the diamond in the piston
(similar to the above step). The process of aligning the diamonds is iterative in nature,
and the above procedure is usually repeated 3-4 times before the diamonds are perfectly
aligned to the rotational center of the cell.
After the alignment was complete, small pieces of sandpaper were used to remove
any debris, and then a q-tip soaked in ethanol was used to thoroughly clean the culets.
This was repeated several times to ensure that the culets were clean and ready for further
procedures. Figure 3.1 shows an unaligned and aligned DAC.
Figure 3.1. Unaligned and aligned DAC
3.3 Gasket Preparation
The introduction of a gasket into the diamond anvil apparatus, which was first
demonstrated by Van Valkenburg [50], is a very important development in the history of
the DAC; for it is this discovery which allows the use of the DAC as a quantitative tool
for high pressure research. The gasket performs two functions in a high pressure
16
experiment. With a hole pierced it provides a chamber for the sample to be studied, and
also gives lateral support to the diamond anvils [51]. This support is given by the gasket
extruding from the sample chamber around the side of the diamond anvils. The
extrusion, acting as a supporting ring, creates stress concentrations towards the sample at
the edge of the culets that prevent the motion of the gasket material between the anvils as
well as anvil failure [35]. Below ~5 GPa, the gasket does not display significant
deformation and beyond ~5 GPa, the gasket material yields and undergoes large
deformation and flows out of the sample chamber to form a curved feature. The flow rate
decreases after ~50 GPa due to the bending of the diamond anvils [37]. This process is
illustrated in Figure 3.2.
(a) (b)
Figure 3.2. Deformation of gasket under pressures during indentation; (a) below ~5 GPa; (b) above ~5 GPa
The first step in preparing the gasket was to create an indentation at its center by
subjecting the gasket to a pressure predetermined by the designated maximum pressure in
the experiment. This was done by using the DAC in conjunction with a small ruby chip
to measure the indentation pressure. A table showing desired pressures to be obtained in
an experiment with their corresponding indentation pressures is displayed on the
17
following page [37]. With the maximum pressure being 41 GPa in this experiment, the
indentation pressure was 20 GPa. After the gasket was indented, it was removed from
the DAC and a hole was drilled in the center of the indentation as the sample chamber.
This was performed with an electronic drilling machine (EDM)
Table 3.1. Indentation pressures [37]
Maximum Pressure (GPa) Indentation Pressure (GPa)
<30 1/2 Pmax
>30 20
>50 30
An EDM uses electricity as opposed to mechanical methods to machine metals.
In this process, a spark is created between a tool (tungsten bit) and a sample (gasket) of
different voltage polarity when they are brought into close proximity. This spark, which
occurs when a tool discharges current to the sample through a dielectric medium, can
melt a small portion of the sample with sufficient energy [52]. Since the process can be
applied to either soft or hard metals the EDM is ideally suited for drilling high pressure
gasket materials such as rhenium, stainless steel, and inconel with 2-3 µm tolerances [52].
A picture of an EDM is shown in Figure 3.3.
18
Figure 3.3. Electronic drilling machine
In preparation for drilling the hole with the EDM, the indented gasket was placed
on the stage and secured with a small metal mount (positive side of the electric circuit).
Then the wire drilling tool (negative side of the electric circuit) was lowered (z-direction)
until it almost touched the gasket, and the stage was translated (x and y-directions) until
the tool was aligned with the center of the indentation. Off-center alignment could have
19
caused the sample to migrate under load from the center to the edge of the culet, limiting
the highest pressures of the experiment and possibly causing premature failure of the
anvils [52]. After centering, a dielectric organic solvent (ethanol) was dropped onto the
stage and the tool was brought close enough to the gasket to start the spark. The
machining process lasted approximately 3-4 minutes. Figure 3.4 shows the gasket at
different stages of the process.
(a) (b) (c) Figure 3.4. Gasket; (a) before indentation; (b) after indentation;
(c) with machined sample chamber
3.4 Sample Loading
The sample, (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4, was ground into fine grains and
compressed to form a large flake before it was loaded into the sample chamber. This was
done using 1 in3 tungsten carbide blocks. With a pre-drilled gasket centered on the
bottom culet (piston side) and secured with a small piece of wax (which creates no
diffraction peaks), the sample flake was placed in the center of the gasket hole avoiding
contact with the gasket. A small ruby chip was then placed on the culet between the
sample and the gasket in order to measure the pressure during the experiment (see section
2.3). After placement of the sample and ruby, the cylinder side of the DAC was carefully
20
lowered onto the piston, avoiding any impact of the top culet with the sample and ruby.
A diagram explaining this along with a picture of the sample and ruby loaded into the
gasket in this experiment are shown in Figures 3.5 and 3.6, respectively.
Figure 3.5. Schematic of loaded DAC
21
Figure 3.6. Picture of sample and ruby loaded in the gasket
3.5 Pressure Medium
The next step in the experimental procedure is to load the pressure transmitting
medium into the sample chamber. The pressure medium completely fills the spatial voids
in the sample chamber left after loading the sample and pressure calibrator (ruby). The
purpose of the pressure medium is to convert the axial forces applied by the squeezing
mechanism of the DAC to hydrostatic pressure on the sample. It is required to have a
low shear strength (minimizing deviatoric stresses in the sample chamber) and chemical
inertness (non-reactive with the sample). Ideal pressure media are the noble gases, which
fulfill all requirements [14]. Several acceptable pressure media and their respective
hydrostatic limits are listed in Table 3.2 [37].
22
Table 3.2. Pressure media and their hydrostatic limits [37]
Material Hydrostatic Limit (GPa) Condition
Ar2 ~60 Hydrostatic
He ~100 Quasi-hydrostatic
N2 ~13 Hydrostatic
Xe2 ~100 Quasi-hydrostatic
Methanol/Ethanol (4:1) ~12 Hydrostatic
Al2O3 ~100 Quasi-hydrostatic
NaCl ~28 Quasi-hydrostatic
In this experiment, liquefied argon was used, allowing hydrostatic conditions to
be achieved up to 60 GPa. The pressures reached throughout the experiment were well
within the hydrostatic limits of the pressure medium. When loading the pressure
medium, the first step was to loosen the set screws and slightly tighten the main screws,
allowing the culets to come in contact with the sample. At this point reference guidelines
were marked on each screw, with four matching lines being marked on the DAC. These
later allowed the pressure medium inside the sample chamber to be secured without
applying any initial pressure. Next, the main screws were loosened, turning them 180°,
and one set screw was tightened until a slight gap was observed between the culets and
the gasket. If this gap was too large, the sample may have been lost when the pressure
medium filled the sample chamber. The set screw was then loosened to allow the
pressure medium to be contained inside the sample chamber when the main screws were
tightened later in the procedure. The DAC was gently placed in a container which could
withstand cryogenic conditions, avoiding any impulse forces on the sample. This
23
container was placed in an insulating shell, and a helical shaped copper tube which was
connected to an argon tank at one end and entered the container at the other end was
inserted between them. The tank valve was opened and the argon was allowed to flow
inside the container for several minutes. Next, a cover was placed over the container to
isolate the DAC from dry air (completely exhausted from the container by having a lower
molecular weight than argon, 28.97g/mol and 39.94g/mol, respectively), which could
have condensed upon cryogenic cooling and entered the sample chamber. Liquid nitrogen
was poured between the two containers submerging the copper tube. At this point the
argon began to liquefy due to conductive heat transfer with the liquid nitrogen, and was
allowed to flow until the entire sample chamber was submerged. After submersion was
complete, the liquefied argon continued to flow until boiling (caused by the room
temperature DAC) stopped. Then the main screws were tightened 180° to their original
position, containing the pressure medium inside the sample chamber. Finally, the DAC
was removed from the container and allowed to reach room temperature. A 2-d
cross-sectional schematic of the pressure medium loading apparatus is shown in
Figure 3.7.
24
Figure 3.7. Pressure medium loading apparatus
3.6 Pressure Measurement
A small ruby chip was placed in the sample chamber and was used to measure the
pressure throughout the experiment. The value of the wavelength of the ruby R1 line was
used before each diffraction measurement in conjunction with Equation 2.5 (see section
2.3) to determine the pressure for that particular run. The resolution of the R1 and R2
lines together with their intensity ratio can give a good measure of hydrostaticity. In an
ideal hydrostatic condition the distance between the R1 and R2 lines is 1.5 nm, and the
intensity ratio
15
2
1 =R
R
I
I. (3.1)
When pressure becomes non-hydrostatic, the two peaks begin to overlap until
only one peak is observed. Figure 3.8 shows the measured ruby spectrum at 41.2 GPa in
25
this experiment. It should be noted that although this does not meet the criteria for ideal
hydrostatic conditions, due to both peaks being present with minimal overlap at the
highest pressure reached, that hydrostatic conditions were achieved throughout the
experiment.
702.5 705.0 707.5 710.0 712.5300
400
500
600
700
800
900
R2 Line
R1 Line
In
tens
ity
Wavelength (nm)
Figure 3.8. Observed ruby spectra at 41.2 GPa
3.7 Energy Dispersive X-ray Diffraction Measurements
The sample was probed using EDXRD techniques at the superconducting wiggler
beam line X17B3, National Synchrotron Light Source, Brookhaven National Laboratory.
A schematic of the system is shown in Figure 3.9. The X-ray was focused to
approximately 25 µm x 30 µm using two pairs of tungsten slits. In order to align the
sample with the X-ray beam, the horizontal and vertical X-ray beam intensity
26
distributions transmitted through the DAC were measured as a function of motor position
by scanning the DAC stage. The position of the sample and the gasket hole were shown
in the obtained two dimensional maps of the transmitted X-rays. An example of the
transmission curve during a scan is shown in Figure 3.10. Using this method the center
of the gasket hole could be determined, which was used as a reference position, according
to which the desired position could be located to the X-ray. The accuracy of the motor
used is 1µm, which is sufficient for the experimental requirements.
Figure 3.9. EDXRD system
The data was collected with a solid-state germanium CCD detector with a 2θ
angle of 8° being used throughout our experiment. Figure 3.11 illustrates the transmitted
X-ray beam being reflected from the sample with the corresponding diffracted beam and
2θ angle. Data accumulation times were approximately 12 minutes. Crystals have a
tendency to orient along certain directions in a DAC at elevated pressures [53]. When
this occurs, the diffraction signal may be partially or completely lost. Using the
27
continuous rotation method allowed an average diffraction spectrum to be collected
within the covered angles. The DAC was continuously rotated (0.5°/second)
perpendicular to the X-ray beam while diffraction patterns were recorded to overcome the
coarse crystal effect. In our experiment, the rotation stage had 0.023° on-axis and
70 µrad tilt angle accuracies, which was sufficient to keep the sample precisely aligned
with the X-ray beam [53].
-5.0 -4.9 -4.8 -4.7 -4.6 -4.50
1000
2000
3000
4000
5000
diameter
diamond anvil culet diameter
gasket hole
Inte
nsity
(co
unts
)
Distance (mm)
Figure 3.10. X-ray beam intensity distribution
28
Figure 3.11. Transmitted and diffracted X-ray with 2θ angle
29
CHAPTER IV
RESULTS AND DISCUSSION
4.1 Results and Discussion
4.1.1 Lattice Change of Chromite under Pressure
From the EDXRD measurements, we collected the X-ray diffraction patterns to
41.2 GPa. An X-ray diffraction pattern of chromite at 3.5 GPa is shown in Figure 4.1.
We observed (3 1 1), (2 2 2), (4 0 0), (5 1 1), (3 3 3), (6 0 0), and (4 4 2) peaks in our
measurements as shown in the figure. Figure 4.2 shows diffraction patterns at 3.5, 9.7,
16, 20.2, and 25.3 GPa. It should be noted that the indexed peaks shift linearly with
pressure to 25.3 GPa. A Peakfit program (Peakfit v4.11) was used to analyze the
diffraction patterns and determine peak positions at different pressures. After
determining the peak positions in keV (energy), the lattice spacings of the peaks were
obtained using the procedure in section 2.2. Within this pressure range (<25.3 GPa) the
diffraction patterns can all be indexed into the face centered cubic (fcc) structure, with
the cell parameter varying in response to pressure. The relationship of the d-spacings of
these peaks with pressure measured to 25.3 GPa is shown in Figure 4.3. Using the
d-spacings of the (3 1 1), (2 2 2), (4 0 0), (5 1 1), (3 3 3), (6 0 0), and (4 4 2) planes in
conjunction with a refinement software (Robert Downs, University of Arizona); the cell
parameter, a, and volume of the unit cell, V, of chromite were determined to different
pressures. These values are shown in Table 4.1. The numbers in parentheses are the
30
error that correlate to the last digit. The relationship of the cell parameter, a, with
increasing pressure is shown in Figure 4.4.
30 40 50 60 70
0
500
1000
1500
2000
(Ar)
(Ar)
(600
,442
)
(511
,333
)
(400
)
(222
)(3
11)
Inte
nsity
Energy (keV) Figure 4.1. X-ray diffraction pattern at 3.5 GPa. Numbers in the brackets represent the (h k l) values of the corresponding peaks. Peaks not marked are from the X-ray diffraction
system.
31
3.5 GPa
(6 0
0,4
4 2
)
(5 1
1,3
3 3
)
(3 1
1)
Energy (keV)
9.7 GPa
20.2 GPa
16 GPa
25.3 GPa
40 50 60 70
(2 2
2)
(4 0
0)
Inte
nsity
Figure 4.2. X-ray diffraction patterns at different pressures. Numbers in the brackets
represent the (h k l) values of the fcc chromite.
5 10 15 20 251.2
1.3
1.4
1.5
1.6
1.7
1.8
1.9
2.0
2.1
2.2
2.3
2.4
2.5
2.6
(600),(442)
(511),(333)
(400)
(222)
(311)
d-sp
acin
g (Å
)
Pressure (GPa)
Figure 4.3. Effect of pressure on the d-spacings of the spinel chromite
32
Table 4.1. Refinement results
Pressure (GPa) Cell Parameter: a (Å) Unit Cell Volume: V (Å3)
0.0001 8.3106(28) 573.98(58) 3.5 8.2968(36) 571.14(75)
5.2 8.2696(44) 565.53(92)
9.7 8.243(11) 560.2(23)
12.7 8.216(14) 554.6(29) 16 8.2112(73) 553.6(14)
18.2 8.2255(68) 556.5(13) 20.2 8.2265(88) 556.7(18) 22.9 8.1931(61) 549.9(12) 25.3 8.209(16) 553.3(32)
0 5 10 15 20 258.18
8.20
8.22
8.24
8.26
8.28
8.30
8.32
cell
para
met
er: a
(Å
)
Pressure (GPa)
Figure 4.4. Cell parameter reduction with pressure
33
4.1.2 Equation of State of the Spinel Chromite and Pressure Medium
The bulk modulus is defined as the measure of compressibility of a material and
its first pressure derivative is the measure of the rate at which it becomes stiff as it is
compressed [36]. The bulk modulus of spinel chromite (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4
was calculated using the third order Birch-Murnaghan equation of state (EOS)
( )
−
−−
−
= 14'
43
123 3
2
03
5
03
7
0
v
vK
v
v
v
vKP OTOT . (4.1)
After refinement was performed, the values of pressure (with error approximated at 0.05
GPa) and their corresponding volumes were input into BULK software (Robert Downs,
University of Arizona), which was used to obtain the bulk modulus KOT and it’s first
pressure derivative K′OT. These values were found to be KOT =197±19 GPa with
K′OT=66±12 when fitting data to 16 GPa, and KOT =260±22 GPa with K′OT =51±9 when
fitting data to 25.3 GPa. These values when fit to the experimental data are shown in
Figure 4.5. The large difference in bulk moduli when fitting data to 16 and 25.3 GPa can
be attributed to the increase in volumes at 18.2 and 20.2 GPa. This could possibly be due
to a phase transition initiating at 18.2 GPa. Thus, we believe that the KOT =197±19 GPa
reflects the bulk modulus of the low pressure chromite phase.
34
0 5 10 15 20 25545
550
555
560
565
570
575
Fit data below 16 GPa
Fit data below 25.3 GPa
Vol
ume(
Å3 )
Pressure (GPa) Figure 4.5. Equation of state of chromite. The dashed line shows the EOS using
data to 16 GPa, the solid line shows the EOS using data to 25.3 GPa.
The compressibility of the pressure medium, argon, was also investigated. This
was done with the same procedure as for chromite, but with the (1 1 1) and (2 0 0) planes
being used. Argon is known to transform from a liquid to a single crystal solid at
1.15±.05 GPa [54]. Using Equation 4.1, the equation of state of argon was determined to
20.2 GPa. The bulk modulus was found to be KOT=2.97 GPa when K′OT =9, which agrees
with previous literature [54, 55]. The equation of state is shown in Figure 4.6, with
measured volumes at pressures.
35
0 5 10 15 2070
80
90
100
110
120
130
140
150
160
KOT
=2.97 GPaK'
OT=9
Vol
ume
(Å3 )
Pressure (GPa)
Figure 4.6. Equation of state of argon with measured volume at pressures
4.1.3 Pressure Induced Phase Transformation of Chromite
(Fe0.44Mg0.56)(Cr0.89Al0.11)2O4 is known to have a cubic fcc structure at ambient
conditions with space group Fd3m [56]. We found that the indexed peaks shift linearly
with pressure to 25.3 GPa. At 28.2 GPa, the diffraction patterns change abruptly and can
no longer be indexed into the fcc structure. Figure 4.7 shows the change of the pattern
when pressure increased to 28.2 GPa. Figure 4.8 shows the relation of the d-spacings of
the indexed peaks with pressure. It should be noted that the d-spacings change drastically
at 28.2 GPa, indicating a structural phase transition at this pressure. These new d-
spacings can fit to two different orthorhombic structures, the CF and CT structures,
36
which spinels have been established to transform to at high pressures [32]. However, our
current data cannot distinguish the structures. Further investigation is required for
clarification.
16 GPa
(6 0
0,4
4 2
)
(5 1
1,3
3 3
)
(3 1
1)
Energy (keV)
28.2 GPa
30.1 GPa
40 50 60 70
(2 2
2)
(4 0
0)
Inte
nsity
Figure 4.7. Comparison of the X-ray diffraction pattern before and after the phase
transformation
37
5 10 15 20 25 30 35 40 45
1.3
1.4
1.5
1.6
1.7
1.8
1.9
2.0
2.1
2.2
2.3
2.4
2.5
2.6
(600,442)
(511,333)
(400)
(222)
(311)
d-sp
acin
g (Å
)
Pressure (GPa)
Figure 4.8. d-spacings as a function of pressure, emphasizing the structural
change at 28.2 GPa and above
4.2 Conclusion
A high pressure energy dispersive X-ray diffraction study was carried out
to explore the isothermal compressibility and possible pressure-induced phase
transformation of (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4 spinel chromite. The sample, which is an
fcc structure at ambient conditions [56], was able to be indexed into the fcc structure
using the (3 1 1), (2 2 2), (4 0 0), (5 1 1), (3 3 3), (6 0 0), and (4 4 2) planes in
conjunction with a refinement software to 25.3 GPa. The values of the d-spacings of the
38
indexed peaks shift linearly to 25.3 GPa, as seen in Figure 4.3. Then, using BULK
software (Robert Downs, University of Arizona), two bulk modulus values for the sample
were obtained. The bulk modulus was calculated to be KOT =197±19 GPa with
K′OT=66±12. This values when transposed on the experimental data is shown in Figure
4.5. Due to the increase in the volume of the unit cell at 18.2 and 20.2 GPa, we believe
that KOT =197±19 GPa is the accurate value of the bulk modulus for the low pressure
phase of the spinel chromite. It was also found that (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4
transforms to another structure at 28.2 GPa. As evidenced by the pattern, the sample can
be indexed into two different orthorhombic structures, the CaFe2O4 and CaTi2O4 type
structures. The abrupt shifts in the d-spacings of the diffraction peaks are shown in
Figure 4.8. In order to properly identify the structure that (Fe0.44Mg0.56)(Cr0.89Al0.11)2O4
spinel chromite transformed to in this experiment, further investigations need to be done.
Furthermore, for better understanding the mechanisms of the spinel structure, an
extensive study of the structural, magnetic, and thermodynamic properties of numerous
spinels should be performed.
39
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44
APPENDIX
OTHER WORKS BY THE AUTHOR
A. White, Y. Ma, R. Aksoy, E. Selvi, and J. Sandhu, X-ray Diffraction Measurements of
Chromite to 41 GPa, Journal of Physics and Chemistry of Solids, submitted (2005). A. White, Y. Ma, R. Aksoy, E. Selvi, and J. Sandhu, High Pressure X-ray Diffraction
Study of Chromite [(Fe0.44Mg0.56) (Cr0.89Al0.11)2O4] to 41 GPa, ASME International Southwest Region X 2005 Graduate Student Technical Conference, submitted. Y. Ma, J. Liu, C. Gao, and A. White, An in situ high pressure X-ray Diffraction Study of
CaCu3Ti4O12 Perovskite: Evidence of a stiffer Grain Surface, Physics Review Letter, submitted (2005). C. Gao, Y. Han, Y. Ma, A. White, and G. Zou, High Pressure in situ Resistivity
Measurement in a Diamond Anvil Cell, Review of Scientific Instruments, submitted (2005). E. Selvi, Y. Ma, R. Aksoy, A. Ertas, A. White, and J. Sandhu, High Pressure X-ray
Diffraction Study of WS2, Journal of Physics and Chemistry of Solids, submitted (2005). R. Aksoy, Y. Ma, E. Selvi, M. Chyu, A. Ertas, and A. White, Equation of State
Measurement of Molybdenum Disulfide to 38.8 GPa, Journal of Physics and Chemistry of Solids, submitted (2005). E. Selvi, Y. Ma, R. Aksoy, A. Ertas, A. White, and J. Sandhu, Equation of State
Measurement of Tungsten Disulfide to 25 GPa, ASME International Southwest Region X 2005 Graduate Student Technical Conference, submitted. R. Aksoy, Y. Ma, M. Chyu, A. Ertas, and A. White, High Pressure X-ray Diffraction
Study of Molybdenum Disulfide, ASME International Southwest Region X 2005 Graduate Student Technical Conference, submitted.
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