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CHAPTER 3
EXPERIMENTAL BACKGROUND AND PROCEDURES
Many fabrication methods have been used in the production of metal
oxide and metal nitride semiconductor sensors. Factors that must be considered
when selecting the production technique include; expense (if the films are
expensive, the demand will be low and will have only limited applications),
purity, porosity (if the material is highly porous, the surface area available to the
gas for interaction will be far higher, giving a higher sensitivity), reliability and
reproducibility. Common techniques for making the metal oxide and nitride
films for gas sensors are mainly chemical vapour deposition (CVD), screen-
printing of ceramic powders, sol-gel techniques and physical vapour deposition
(PVD), electron beam and sputtering. In order to fabricate the high quality ITO
thin films, several methods have been reported, such as rf magnetron sputtering
[82-84], and dc magnetron sputtering [85-87]. The effects of the deposition
parameters on properties of aluminum nitride thin films were investigated by dc
[88, 89] and rf sputtering [90-95].
In the present work, ITO and AlN thin films have been prepared by
magnetron sputtering. Sputtering may be a more desirable process for the
deposition of oxide and dielectric materials due to its processing simplicity and
scalability in the semiconductor industry. The advantages of reactive magnetron
sputtering include inexpensive equipment, low temperature growth conditions
and ease of deposition. It is important to be able to control the crystal
orientation and crystalline quality of the film for many applications. Properties
of films are strongly dependent on deposition parameters such as target power,
growth temperature, sputtering pressure and gas compositions [96-102].
3.1 SPUTTERING
Magnetron sputtering is a thin film deposition technique based on the
physical sputtering effects caused by the bombardment of a target material with
accelerated ions produced within glow discharge plasma. A wide variety of thin
film materials, from metals to insulators, may be produced using this technique
[88]. Usually the thin film composition will be determined exclusively by the
elements composing the target, since the only elements occurring in the gas
phase are the noble gas ions used to generate the plasma and other particles
ejected from the target as the result of the sputtering process. In some cases a
reactive element may be introduced in the gas phase that will interact with the
deposited elements; this latter case is called reactive sputtering. In order to
understand the thin film growth processes and the dependence of its
characteristics on the system parameters, it is necessary to know how the
particles are removed from the target and how they interact on the substrate
surface. Therefore in the following sections ion production, sputtering
mechanisms and film growth will be briefly explained, before presenting the
system used to produce the sensor film layers and the correlations found with
the deposition parameters.
3.1.1 Plasma process
Ions used in planar magnetron sputtering systems are generated by glow
discharge processes. A glow discharge may be established when a potential is
applied between two electrodes in a gas. Once established two or three different
regions can be clearly distinguished between the electrodes. Close to the
cathode there is a dark region that exists also near the anode although the latter
is generally too thin to be observed. Next there is negative glow region and if
the separation between the electrodes is higher than a few times the dark space
thickness, a positive column develops between the negative glow and the anode.
The positive column is the region that more closely resembles a plasma. The
plasma does not take a potential between those of the electrodes, but rather
acquires a potential slightly higher than that of the anode. Inside the plasma, as
expected, the electric field is very low. The main potential difference is
therefore observed at the sheaths next to each of the electrodes. The role of the
magnetron is forming electron traps that help to sustain the discharge.
Without the magnetron, the electrons emitted from the cathode by ion
bombardment are accelerated nearly to the full applied potential in the cathode
dark space and enter the negative glow, where they collide with the gas atoms
producing the ions required to sustain the discharge. As the electron mean free
path increases with gas pressure decrease, at low pressures the ions will be
produced far from the cathode where the chances of being captured by the walls
are high. At the same time many primary electrons (the ones emitted from the
cathode) reach the anode with high energy, inducing secondary electron
emission. Therefore, ionization efficiencies are low and self sustained
discharges cannot be maintained in planar diodes at pressures below 1:3Pa
[103]. Currents are also limited since voltage increases the primary electron
energy and consequently their mean free path. At high pressures the sputtered
atom transport is reduced by scattering, which at some point starts to force a
decrease in the deposition rate. On the other hand, with the magnetron system
configuration, the primary electron motion is restricted to the vicinity of the
cathode and thereby ionization efficiency is increased. This effect is easily
obtained imposing a magnetic field parallel to the cathode surface and thus
normal to the electric field.
In a planar configuration, the E x B motion causes the discharge to be
swept to one side. This difficulty can be overcome using cylindrical cathodes,
which allow E x B to close on them. Planar magnetrons can be achieved by
placing the magnets, directly behind the cathode, in a configuration such that at
least one region in front of the cathode surface has a closed path which is
perpendicular to the magnetic field lines that are parallel to the surface.
Although there are many variations in geometry, all have in common a closed
path or region in front of a mostly flat cathode surface, where the magnetic field
is normal to the electric field. Bounding this region the magnetic field lines
enter the cathode surface. Ideally, at the entry points the field lines are
perpendicular to the cathode surface. The ionization region is thus confined to
an area adjacent to the cathode surface by one or more endless toroidal electron
trapping regions, bounded by a tunnel shaped magnetic field.
3.1.2 Magnetron sputtering
When an ion impinges on the cathode surface several processes may take
place: the incident ion will either be implanted or reflected, probably as a
neutral and with a large loss of energy; a target atom may be ejected (sputtered);
the ion impact and the resulting cascade will cause an amount of structural
reordering in the surface layers and secondary electrons may be ejected. Of the
mentioned processes the most important for the thin film formation is the
sputtering process.
The sputtering yield, S, is defined as the number of atoms ejected from
the target per incident particle. Important factors that affect the sputtering yield
include surface structure, mass of the bombarding ion and incident energy. The
sputtering process is rather insensitive to temperature, and in certain cases, there
is even a decrease in S with increasing target temperature [104]. Near the
threshold energy, the sputtering yield rises rapidly with ion energy increase.
From about 100 eV upwards, the sputtering yield increases almost linearly with
ion energy, where the values begin to be large enough to be useful for film
deposition. With further increase in ion energy the sputtering yield reaches a
maximum and starts to decrease, mainly due to the larger penetration depth of
the ions within the target surface. For light ions, such as hydrogen or helium, the
maximum of S is reached at a few thousand eV, since this particle penetrate
rather easily. For heavy ions, such as xenon or mercury, the maximum may not
be attained until values near 50 KeV or higher. The sputtering yield dependence
on the atomic number of the target atoms for various inert gas ions shows some
kind of periodicity.
A sputtering yield increase is observed, for instance, when the target
material changes from group III-B to group I-B transition metals, but a steep
decrease follows from a metal of group I-B to the metal of group III-B of the
next period (row of the periodic table). This can be qualitatively understood
looking at the electronic structure of transition metals. As the d-orbitals are
filled by electrons, collisions among atoms within the solid become more
elastic, this results in more efficient energy transfer. On the other hand the bond
energies between the atoms become weaker and thus the removal of the atoms is
easier. Neutral gas atoms or molecules may also initiate target material
sputtering, although in plasma-solid interactions these processes have lesser
importance due to the extremely small momentum of the neutral particles.
3.1.3 Growth kinetics of thin film
In sputtering deposition as in other standard vacuum deposition
processes, the material arrives at the substrate mostly in an atomic or molecular
form. Using the kinetic theory of gases, it is possible to estimate the frequency
with which gas particles impinge on a surface, υ, when the gas phase pressure is
P
…. (3.1)
In equation 3.1, m is the mass of the gas particles, K the Boltzmann constant
and T the temperature. Considering that for air the mean particle mass is 4.8 x
10-23
g, collision frequency will be approximately 3 x 1024
cm-2
s-1
at 25 0C and
1 atm. Given that a perfectly smooth surface of 1 cm3 has about 10
15 atoms,
when immersed in a gas at 1 atm pressure, each atom on the surface will be hit
about 109 times each second. At 5 x 10
-3 mbar, collision frequency will be
reduced to 1.5 x 1019
cm-2
s-1
which is still a very high frequency. In the case of
sputtering the particles that will interest to the film growth will be the ones
evaporated from the target and these will have a much lower collision
frequency.
The condensed particles may diffuse around the surface, with a motion
determined by their binding energy to the substrate, may be incorporated into
the lattice or evaporate. Given the high collision frequency of the gas particles
inside the deposition chamber these will have a non-negligible influence on the
adsorbed particles diffusion. The diffusion process may lead to adsorption,
particularly at special site edges or other defects, or the diffusing particle may
desorb. During these processes, characteristic activation energies have to be
overcome. The corresponding activation energies for adsorption or diffusion
depend on the atomic details of each process. Besides adsorption and surface
diffusion, nucleation of more than one adsorbed particle might occur.
Interdiffusion of adsorbed particles with the substrate often happen leading to
film-substrate interface smoothing. In thermodynamic equilibrium all processes
take place in two opposite directions at equal rates. Therefore, in equilibrium no
net film growth would be observed, so that layer growth must be a non-
equilibrium kinetic process.
The final macroscopic state of the system may not be the most stable one,
since it is kinetically determined. In general however, certain parts of the overall
process may be kinetically forbidden, whereas others may be in local
thermodynamic equilibrium. In this case equilibrium arguments may be applied
locally even though the whole growth process is a non-equilibrium one. Given
this fact, a global theory of film growth requires a description in terms of rate
equations for each of the processes taking place at the surface. Instead of
following a more theoretical atomistic approach it is possible to consider the
film growth mechanism using a more phenomenological perspective.
Usually, three distinct modes of film growth may be considered: layer by
layer growth mode or Frank-Vander Merve mode; island growth mode or
Vollmer-Weber mode and layer-plus island growth mode, that is also called
Stransky-Krastanov mode; each named after the -investigators associated with
their initial description. In layer by layer growth mode the interaction between
the substrate and the layer atoms is stronger than between neighbouring atoms.
Each new layer starts to grow, only when the last one is completed. If, on the
contrary, the interaction between neighboring atoms is stronger than the
overlayer-substrate interaction, the particles will rather form aggregates over the
surface that grow in size and eventually coalesce during film growth. This
makes up the island growth mode. The layer-plus-island growth mode is an
intermediate case where the film starts to grow layer by layer in a first stage and
only afterwards begins the formation of island agglomerates. In island growth
mode, each island is usually a single crystal or contains just a few crystals.
On a polycrystalline or amorphous substrate, the orientation of each
island will be random and the resultant film will be polycrystalline. On single
crystal substrates, the islands orientations may be constrained to a given
direction by the substrate structure, so that growth and coalescence leads to the
formation of a single crystal film. This case is usually known as epitaxy. If
surface atoms have high mobility, they have greater opportunity of finding low
energy positions consistent with crystal growth. Knowing that mobility is
increased by surface temperature, it is expected that higher substrate
temperature will promote crystal growth. The same effect can be achieved by
reducing the deposition rate, which gives more time to the adsorbed species to
find an energetically favourable lattice position. Epitaxial growth was also
found to be promoted by electron or ion bombardment and increased energy of
deposited atoms [100].
The environmental conditions around the substrate during magnetron
sputtering deposition deserve also to be mentioned, since they will inevitably
affect the film structure obtained. Namely, it was ignored in the above
description the effect of the energy of the impinging sputtered atoms, as well as
the effect of many other particles that may impact on the surface. In first place
there might be contaminants arriving at the substrate. These may result from an
internal source, such as outgassing from a heating substrate, or by an external
source such as the sputtering gas. If the contaminant atoms are chemically
active, the contamination will be particularly effective and can only be
minimized by reducing the contaminant partial pressure. If the contaminant
source is outgassing, the system may have to be evacuated to a higher vacuum
or the sources of outgassing heated in order to reduce the outgassing rate and
guarantee a sufficiently low partial pressure of the contaminant during
deposition. On the other hand, if the contaminant comes with the sputtering gas
there is no way to reduce its partial pressure without affecting simultaneously
the sputtering gas pressure. Thus it is very important to use high purity
sputtering gases.
The sputtering gas atoms might also become part of the deposited film.
Although the sputtering gas used is usually an inert gas, given its high partial
pressure when compared with that of the sputtered atoms it is not surprising that
some of these atoms happen to be trapped in the growing film. Inert gas atoms,
are only expected to be physisorbed, so if substrate temperature is increased
during deposition, they are less likely to be adsorbed and at the same time more
likely to be subsequently desorbed. However, there exists an appreciable
difference between the interaction of fast gas particles and that of thermal
neutrals with the surface. Energetic neutrals may result from the reflection and
neutralization of ions that impinge on the target. These neutrals, arriving at the
substrate, have much higher probability to be embedded in the growing film
than thermal neutrals. In fact, it has been observed that nickel films deposited by
sputtering in an argon atmosphere have higher argon content than nickel films
produced in a similar atmosphere, but using evaporation [105]. Positive ions
may also impact on the substrate due to the sheath voltage drop near its surface.
Negative ions and electrons can only reach the substrate if they have
enough energy to cross the space-charge sheath. Once again it is necessary to
distinguish fast from slow particles. Fast negative ions and electrons are
produced in the target and accelerated in the target sheath. These fast particles
can have a major influence on the structure and properties of the growing film
and also cause substrate heating. Finally there are also photons arriving at the
substrate. Photons can be produced by ion or electron bombardment on any
surface or result from relaxation of excited atoms in the glow. In the former case
the photons may have high energy, at most as high as the energy of the
bombarding particle. Such energies may be, in a sputtering system, of the same
order of the accelerating potential at the target, which is usually higher than 200
eV. The main effect of photon bombardment of the substrate will be electron
emission, which may also affect the film growth processes occurring at the
substrate.
3.1.4 Vacuum coating unit
A vacuum coating unit consists of vacuum chamber, rotary pump,
diffusion pump and penning guage.
(a) Rotary oil pump
This pump is most commonly used to produce moderately low pressures
of the order of 10-3
torr. It is widely used in laboratories in vacuum coating
units. The working is based on the principle of displacement of a gas. A portion
of the gas inside a chamber is isolated by a rotating disc and is then compressed
till it attains a sufficiently high pressure and gets discharged to the atmosphere.
As a gas consists of fast moving molecules, the residual gas comes and occupies
the whole space and in turn, also gets removed. This process continues and the
pressure of the chamber keeps on decreasing. The rotary pump consists of a
solid cylinder R called Rotor rotating eccentrically inside a hollow cylinder S
called Stator (Figure 3.1). The stator has an inlet I connected to the chamber to
be evacuated and an outlet O which always open outward only. The rotor is
rotated by an electric motor. The space inside the stator S is divided into two
air-tight compartments by means of a vane V between the inlet and the outlet.
The vane is always tightly pressed against the rotor by means of a spring P. To
avoid any leakage, the whole pump is kept immersed in a special of oil called
vacuum oil or hydrocarbon oil.
The working of the rotary pump can be explained by analyzing, four
successive positions of the rotor R as shown in Figure 3.1. In the first position
Figure 3.1(a) the air or gas from the chamber just enters into the space in
between the cylinder and the rotor R. As it rotates, the space inside the stator is
divided into two parts as in Figure 3.1(b). As the rotor rotates further the
volume of the outlet portion decreases and hence air inside these is further
compressed. Figure 3.1(c) shows the final stage of compression which opens the
valve at the outlet O and the gas is expelled out. Meanwhile, the inlet volume
increases, and hence air enters from the chamber. Thus during each rotation of
the cylinder the air is drawn from the chamber and is removed from it
continuously. Within a few minutes, the pump can produce a low pressure of 10-
3 torr in the chamber.
Fig 3.1(a) Fig 3.1(b) Fig 3.1(c)
Fig 3.1 Schematic diagram of rotary pump
(b) Diffusion Pump
These pumps can produce very low pressure down to 10-7
torr. It cannot
operate directly from the atmospheric pressure but requires force vacuum or
backing vacuum from 10-1
to 10-2
torr. The basic principle used in these pumps
is that in a mixture of gases, the diffusion of gas occurs from a region where its
partial pressure is higher to that where it is lower, irrespective of the total
pressure in the two regions. The diffusion pump is made up of stainless steel
and it consists of a cylindrical body having a boiler at the base with pumping
fluid (Silicone DC 704). A number of nozzle (combination of nozzles and jet)
assembles are arranged inside the cylinder. Various nozzles originate at
different parts of the boiler and are designed such that the pressure rise across
the various jet streams increases progressively as one goes from the vacuum
chamber side to the backing pump side. The temperature of the walls is usually
maintained few degrees below room temperature by water cooled coils.
Figure 3.2 shows the schematic diagram of a diffusion pump. The vapour
from the boiling fluid passes up the cylindrical chimney. It jets out through the
nozzle with high speed being directed at an angle downwards. Molecules of gas
which wander are diffused from the chamber towards the jet stream and will be
struck by vapour molecules of the heated pumping fluid. The molecules are
given a downward motion into the dense part of the vapour jet. The net effect is
to compress the gas to the point where they can be removed by a backing pump.
The compression is carried out by stages by using several nozzles in line. As
each stage handle the same number of molecules, the pressure decreases from
the top most nozzle in the last, the annular spacing between the nozzle and the
pump casing increases in the same direction. The pump fluid must be removed
to the boiler after it has performed its function and hence the water cooling of
the pump casing.
Figure 3.2 Schematic diagram of a diffusion pump
(c) Penning gauge
The penning gauge is widely used for Ultra High Vacuum (UHV)
pressure measurements. In the penning gauge, the filament has dispensed width.
It consists of three electrodes kept inside a bulb and are connected to air tight
seal. This bulb is placed inside a permanent magnet. The opening of the bulb is
connected to the vessel whose pressure is to be measured. The electric field
between the electrodes is verified due to the short distance of separation
between them. Here the electrons are produced by field emission. The magnetic
field is applied perpendicular to the electric field. So the electrons travel in an
elliptical path. These electrons produce more ionization due to their collision
with the gas molecules. The ion current is registered by the milli ammeter in the
external electric circuit. This ion current is the measure of the pressure.
Figure 3.3 Schematic diagram of penning gauge
Figure 3.3 shows the schematic diagram of the penning gauge. The
electrons are generated at the cathode and are accelerated towards the anode.
They pass through the anode ring and are then repelled by the other cathode and
they oscillate back and forth eventually winding up the anode ring. This process
will lead to ionization by collision. These ions impinge upon the cathode
releasing electrons which will maintain the discharge. The effective path of the
electron increases since they take a helical path due to the magnetic field. The
long paths of the electrons, result in the production of many more ions than if
they were able to go directly from the cathode to anode. The positive ions thus
produced are collected by the cathode and the ion current is measured. The ion
current is proportional to the gas pressure in the chamber. The micro ammeter is
calibrated in terms of pressure.
(d) Vacuum chamber
The schematic of the vacuum coating unit is shown in Figure 3.4. The
chamber is pumped to vacuum using a diffusion pump which is able to reduce
the pressure below 10-3
Pa. If the chamber is kept open during a long time
period it will take longer to reach high vacuum pressures because of outgassing.
Heating the chamber walls often accelerates evacuation, by promoting
outgassing. The diffusion pump is backed by a rotary pump that is also used to
do primary vacuum inside the chamber before connecting the diffusion pump.
In order to change the substrates the chamber has to be open, so that usually the
frequency of experiments is dependent on the time required to reach high
pressures inside the chamber. The sputtering gases are fed into the chamber
using two mass flow meters. One is calibrated for argon, other for oxygen. The
maximum flow reached by each mass flow meter is 200 sccm for the argon
device, and 20 sccm for N2. The control and measurement is performed using a
power supply and readout system that permits to set the flow of the mass flow
controller. The substrates are positioned on a stainless steel holder, with suitable
holes that work as masks for the deposition.
Figure 3.4 Schematic diagram of vacuum coating unit
The substrate holder can be fixed at different distances above the target and is
maintained at the same potential as the anode and the chamber walls. It is
possible to insulate the substrate holder electrically in order to apply a voltage
bias to control the charged particles that impinge on the substrates. The
substrate heating is performed using a metallic base weaved with an electrical
resistance. The temperature is measured with a thermocouple inserted into a
hole made in one side of the metallic base and controlled by a temperature
controller.
The setup used to heat and measure the substrate temperature does not
make possible to know the actual substrate temperature, because there is an
unknown temperature gradient between the substrate surface and the point
where the thermocouple is placed. However, if given enough time for the heat
transfer fluxes to stabilize, the temperature conditions can be reasonably
reproduced in repeated experiments and the effect of temperature upon the
films‘ characteristics may be studied. Nevertheless, if the substrates pressure or
the sputtering power is changed, for instance, it is not possible to maintain a
fixed temperature on the substrate over repeated experiments, since the
temperature gradient is very likely to change.
Figure 3.5 shows the photograph of the dc/rf magnetron sputtering unit.
The dc power source is able to operate at a maximum voltage of 500V and to
deliver a maximum current of 5A. The user may set the voltage, the current and
the power between 5% and 100% of respective range. The push on button
arrangement with an LED display provision on the unit was used both to set the
source parameters and read the voltage and current values during operation. Rf
frequency of 13.56 Hz is the maximum frequency prescribed for the unit. Peak
to peak voltage greater than 1000V, current densities of 1 mA/cm2,
discharge pressure of 0.5 to 10 m torr are the typical value range for rf
magnetron sputtering. Pressure inside the chamber is measured using a Pirani
gauge in the pressure range from 105
Pa to 10-1
Pa and using a Penning gauge
in ranges from 10-1
Pa to 10-5
Pa. The Penning gauge is cleaned periodically to
ensure repeatability. If the electrodes of this device are covered by an oxide
layer the measurements stray toward lower pressures.
Figure 3.5 Photograph of the dc/rf sputtering unit
3.2 ANALATICAL INSTUREMENTS AND TECHNIQUE [106]
3.2.1 Rutherford backscattering spectrometry (RBS)
Rutherford Backscattering Spectrometry (RBS) is a widely used nuclear
method for the near surface layer analysis of solids. A target is bombarded with
ions at an energy in the MeV-range (typically 0.5–4 MeV), and the energy of
the backscattered projectiles is recorded with an energy sensitive detector,
typically a solid state detector. RBS allows the quantitative determination of the
composition of a material and depth profiling of individual elements. RBS is
quantitative without the need for reference samples, nondestructive, has a good
depth resolution of the order of several nm, and a very good sensitivity for
heavy elements of the order of parts-per-million (ppm). The analyzed depth is
typically about 2 μm for incident He-ions and about 20 μm for incident protons.
An RBS instrument generally includes three essential components:
An ion source, usually alpha particles (He2+
ions) or, less commonly,
protons.
A linear particle accelerator capable of accelerating incident ions to high
energies, usually in the range 1-3 MeV.
A detector capable of measuring the energies of backscattered ions over
some range of angles.
Figure 3.6 shows the photograph of the RBS instrument used to take the
RBS spectra. Tandem accelerator starts with a source of He- ions and position
the positive terminal at the center of the acceleration tube. A stripper element
included in the positive terminal removes electrons from ions which pass
through, converting He- ions to He
++ ions. The ions thus start out being attracted
to the terminal, pass through and become positive, and are repelled until they
exit the tube at ground. A typical tandem accelerator with an applied voltage of
750 kV can achieve ion energies of over 2 MeV.
Figure 3.6 Photograph of Rutherford backscattering spectrometer
Ions which reach the detector lose some of their energy to inelastic
scattering from the electrons, and some of these electrons gain enough energy to
overcome the band gap between the semiconductor valence and conduction
bands. This means that each ion incident on the detector will produce some
number of electron-hole pairs which is dependent on the energy of the ion. The
energy loss of a backscattered ion is dependent on two processes: the energy
lost in scattering events with sample nuclei, and the energy lost to small-angle
scattering from the sample electrons. The first process is dependent on the
scattering cross-section of the nucleus and thus on its mass and atomic number.
For a given measurement angle, nuclei of two different elements will therefore
scatter incident ions to different degrees and with different energies, producing
separate peaks on an N(E) plot of measurement count versus energy. These
peaks are characteristic of the elements contained in the material, providing a
means of analyzing the composition of a sample by matching scattered energies
to known scattering cross-sections. Relative concentrations can be determined
by measuring the heights of the peaks.
3.2.2 X-ray Powder Diffraction
X-ray powder diffraction (XRD) is a rapid analytical technique primarily
used for phase identification of a crystalline material and can provide
information on unit cell dimensions. The analyzed material is finely ground,
homogenized, and average bulk composition is determined. Max von Laue, in
1912, discovered that crystalline substances act as three-dimensional diffraction
gratings for X-ray wavelengths similar to the spacing of planes in a crystal
lattice. X-ray diffraction is now a common technique for the study of crystal
structures and atomic spacing. X-ray diffraction is based on constructive
interference of monochromatic X-rays and a crystalline sample. These X-rays
are generated by a cathode ray tube, filtered to produce monochromatic
radiation, collimated to concentrate and directed towards the sample. The
interaction of the incident rays with the sample produces constructive
interference (and a diffracted ray) when conditions satisfy Bragg's Law (nλ= 2d
sinθ) (figure 3.7). This law relates the wavelength of electromagnetic radiation
to the diffraction angle and the lattice spacing in a crystalline sample. These
diffracted X-rays are then detected, processed and counted. By scanning the
sample through a range of 2θ angles, all possible diffraction directions of the
lattice should be attained due to the random orientation of the powdered
material. Conversion of the diffraction peaks to d-spacings allows identification
of the mineral because each mineral has a set of unique d-spacings. Typically,
this is achieved by comparison of d-spacings with standard reference patterns.
Figure 3.7 The geometry of the incident X-rays impinging the
sample satisfies the Bragg Equation
X-ray diffractometer consist of three basic elements: an X-ray tube, a
sample holder, and an X-ray detector. X-ray are generated in a cathode ray tube
by heating a filament to produce electrons, accelerating the electrons toward a
target by applying a voltage, and bombarding the target material with electrons.
When electrons have sufficient energy to dislodge inner shell electrons of the
target material, characteristic X-ray spectra are produced. These spectra consist
of several components, the most common being Kα and Kβ. Kα consists, in part
of Kα1 and Kα2. Kα1 has a slightly shorter wavelength and twice the intensity as
Kα2. The specific wavelengths are characteristic of the target material (Cu, Fe,
Mo, Cr). Filtering, by foils or crystal monochrometers, is required to produce
monochromatic X-rays needed for diffraction. Kα1and Kα2 are sufficiently close
in wavelength such that a weighted average of the two is used. Copper is the
most common target material for single-crystal diffraction, with CuKα radiation
= 1.5418 Å. These X-rays are collimated and directed onto the sample. As the
sample and detector are rotated, the intensity of the reflected X-rays is recorded.
When the geometry of the incident X-rays impinging the sample satisfies the
Bragg equation, constructive interference occurs and a peak in intensity occurs.
A detector records and processes this X-ray signal and converts the signal to a
count rate which is then out putted to a device such as a printer or computer
monitor.
The geometry of an X-ray diffractometer is such that the sample rotates in
the path of the collimated X-ray beam at an angle θ while the X-ray detector is
mounted on an arm to collect the diffracted X-rays and rotates at an angle of 2θ.
The instrument used to maintain the angle and rotate the sample is termed a
goniometer. For typical powder patterns, data is collected at 2θ from ~5° to 70°,
angles that are preset in the X-ray scan. Figure 3.8 shows the schematic of the
detection of diffracted X-rays by diffractometer. The photograph of the XRD
unit used for recording the XRD patterns is shown in Figure 3.9.
Figure 3.8 Schematic of the detection of diffracted X-rays by
diffractometer
Figure 3.9 Photograph of X-ray diffraction unit
3.2.3 Scanning electron microscopy
The scanning electron microscope (SEM) uses a focused beam of high-
energy electrons to generate a variety of signals at the surface of solid
specimens. The signals that derive from electron-sample interactions reveal
information about the sample including external morphology (texture), chemical
composition, and crystalline structure and orientation of materials making up
the sample. In most applications, data are collected over a selected area of the
surface of the sample, and a 2-dimensional image is generated that displays
spatial variations in these properties. Areas ranging from approximately 1 cm to
5 microns in width can be imaged in a scanning mode using conventional SEM
techniques (magnification ranging from 20X to approximately 30,000X, spatial
resolution of 50 to 100 nm).
Accelerated electrons in an SEM carry significant amounts of kinetic
energy, and this energy is dissipated as a variety of signals produced by
electron-sample interactions when the incident electrons are decelerated in the
solid sample. These signals include secondary electrons (that produce SEM
images), backscattered electrons (BSE), diffracted backscattered electrons
(EBSD that are used to determine crystal structures and orientations of
minerals), photons (characteristic X-rays that are used for elemental analysis
and continuum X-rays), visible light (cathode luminescence--CL), and heat.
Secondary electrons and backscattered electrons are commonly used for
imaging samples: secondary electrons are most valuable for showing
morphology and topography on samples and backscattered electrons are most
valuable for illustrating contrasts in composition in multiphase samples (i.e. for
rapid phase discrimination). X-ray generation is produced by inelastic collisions
of the incident electrons with electrons in discrete orbital‘s (shells) of atoms in
the sample. As the excited electrons return to lower energy states, they yield X-
rays that are of a fixed wavelength (that is related to the difference in energy
levels of electrons in different shells for a given element). Thus, characteristic
X-rays are produced for each element in a mineral that is "excited" by the
electron beam. SEM analysis is considered to be "non-destructive"; that is, x-
rays generated by electron interactions do not lead to volume loss of the sample,
so it is possible to analyze the same materials repeatedly.
Essential components of all SEM include the following:
Electron Source ("Gun")
Electron Lenses
Sample Stage
Detectors for all signals of interest
Display / Data output devices
Infrastructure Requirements
Power Supply
Vacuum System
Cooling system
Vibration-free floor
Room free of ambient magnetic and electric fields
In a typical SEM, an electron beam is thermionically emitted from an
electron gun fitted with a tungsten filament cathode. Tungsten is normally used
in thermionic electron guns because it has the highest melting point and lowest
vapour pressure of all metals, thereby allowing it to be heated for electron
emission, and because of its low cost. The electron beam, which typically has an
energy ranging from 0.2 keV to 40 keV, is focused by one or two condenser
lenses to a spot about 0.4 nm to 5 nm in diameter. The beam passes through
pairs of scanning coils or pairs of deflector plates in the electron column,
typically in the final lens, which deflect the beam in the x and y axes so that it
scans in a raster fashion over a rectangular area of the sample surface. When the
primary electron beam interacts with the sample, the electrons lose energy by
repeated random scattering and absorption within a teardrop-shaped volume of
the specimen known as the interaction volume, which extends from less than
100 nm to around 5 µm into the surface.
The size of the interaction volume depends on the electron's landing
energy, the atomic number of the specimen and the specimen's density. The
energy exchange between the electron beam and the sample results in the
reflection of high-energy electrons by elastic scattering, emission of secondary
electrons by inelastic scattering and the emission of electromagnetic radiation,
each of which can be detected by specialized detectors. The beam current
absorbed by the specimen can also be detected and used to create images of the
distribution of specimen current. Electronic amplifiers of various types are used
to amplify the signals, which are displayed as variations in brightness on a
cathode ray tube. The raster scanning of the CRT display is synchronized with
that of the beam on the specimen in the microscope, and the resulting image is
therefore a distribution map of the intensity of the signal being emitted from the
scanned area of the specimen. The image may be captured by photography from
a high-resolution cathode ray tube, but in modern machines is digitally captured
and displayed on a computer monitor and saved to a computer's hard disk.
Figure 3.11 shows the photograph of the Scanning electron microscopy used to
take SEM image.
Figure 3.10 Schematic diagram of the scanning electron microscope.
Figure 3.11 Photograph of scanning electron microscope
3.2.4 Fourier Transform Infrared spectrophotometer
FT-IR stands for Fourier Transform Infrared, the preferred method of
infrared spectroscopy. In infrared spectroscopy, IR radiation is passed through a
sample. Some of the infrared radiation is absorbed by the sample and some of it
is passed through (transmitted). The resulting spectrum represents the molecular
absorption and transmission, creating a molecular fingerprint of the sample.
Like a fingerprint no two unique molecular structures produce the same infrared
spectrum. This makes infrared spectroscopy useful for several types of analysis.
The interferometer produces a unique type of signal which has all of the infrared
frequencies ―encoded‖ into it. The signal can be measured very quickly, usually
on the order of one second or so. Thus, the time element per sample is reduced
to a matter of a few seconds rather than several minutes. Figure 3.12 and Figure
3.13 shows the schematic diagram and photograph of FTIR-interferometer
system used to take the FTIR spectra.
Most interferometers employ a beamsplitter which takes the incoming
infrared beam and divides it into two optical beams. One beam reflects off of a
flat mirror which is fixed in place. The other beam reflects off of a flat mirror
which is on a mechanism which allows this mirror to move a very short distance
(typically a few millimeters) away from the beam splitter.
Figure 3.12 Schematic diagram of FTIR-spectrometer system
Figure 3.13 Photograph of Fourier transform infrared spectrometer
The two beams reflect from their respective mirrors and are recombined
when they meet back at the beamsplitter. Because the path that one beam travels
is a fixed length and the other is constantly changing as its mirror moves, the
signal which exits the interferometer is the result of these two beams
―interfering‖ with each other. The resulting signal is called an interferogram
which has the unique property that every data point (a function of the moving
mirror position) which makes up the signal has information about every infrared
frequency which comes from the source. This means that as the interferogram is
measured; all frequencies are being measured simultaneously. Thus, the use of
the interferometer results in extremely fast measurements.
Because the analyst requires a frequency spectrum (a plot of the intensity
at each individual frequency) in order to make identification, the measured
interferogram signal cannot be interpreted directly. A means of ―decoding‖ the
individual frequencies is required. This can be accomplished via a well-known
mathematical technique called the Fourier transformation. This transformation
is performed by the computer which then presents the user with the desired
spectral information for analysis. The normal instrumental process is as follows:
Source: Infrared energy is emitted from a glowing black-body source.
This beam passes through an aperture which controls the amount of
energy presented to the sample (and, ultimately, to the detector).
Interferometer: The beam enters the interferometer where the ―spectral
encoding‖ takes place. The resulting interferogram signal then exits the
interferometer.
Sample: The beam enters the sample compartment where it is transmitted
through or reflected off from the surface of the sample, depending on the
type of analysis being accomplished. This is where specific frequencies
of energy, which are uniquely characteristic of the sample, are absorbed.
Detector: The beam finally passes to the detector for final measurement.
The detectors used are specially designed to measure the special
interferogram signal.
Computer: The measured signal is digitized and sent to the computer
where the Fourier transformation takes place. The final infrared spectrum
is then presented to the user for interpretation and any further
manipulation.
Because there needs to be a relative scale for the absorption intensity, a
background spectrum must also be measured. This is normally a
measurement with no sample in the beam. This can be compared to the
measurement with the sample in the beam to determine the ―percent
transmittance.‖ This technique results in a spectrum which has all of the
instrumental characteristics removed. Thus, all spectral features which are
present are strictly due to the sample. A single background measurement
can be used for many sample measurements because this spectrum is
characteristic of the instrument itself.
3.2.5 Ultraviolet - Visible spectrophotometer
Molecules containing π-electrons or non-bonding electrons (n-electrons)
can absorb the energy in the form of ultraviolet or visible light to excite these
electrons to higher anti-bonding molecular orbitals [106] . The more easily
excited the electrons (i.e. lower energy gap between the HOMO and the
LUMO) the higher the wavelength of light it can absorb. The instrument used in
ultraviolet-visible spectroscopy is called a UV/Vis spectrophotometer. The UV-
visible spectrophotometer is configured to measure reflectance. In this case, the
spectrophotometer measures the intensity of light reflected from a sample (I),
and compares it to the intensity of light reflected from a reference material (Io).
The ratio I / Io is called the reflectance, and is usually expressed as a percentage
(%R). The basic parts of a spectrophotometer are a light source, a holder for the
sample, a diffraction grating in a monochromator or a prism to separate the
different wavelengths of light, and a detector. The radiation source is often a
Tungsten filament (300-2500 nm), a deuterium arc lamp, which is continuous
over the ultraviolet region (190-400 nm), Xenon arc lamps, which is continuous
from 160-2,000 nm; or more recently, light emitting diodes (LED) [100] for the
visible wavelengths. The detector is typically a photomultiplier tube, a
photodiode, a photodiode array or a charge-coupled device (CCD).
Single photodiode detectors and photomultiplier tubes are used with
scanning monochromators, which filter the light so that only light of a single
wavelength reaches the detector at one time. The scanning monochromator
moves the diffraction grating to ―step-through‖ each wavelength so that its
intensity may be measured as a function of wavelength. Fixed monochromators
are used with CCDs and photodiode arrays. As both of these devices consist of
many detectors grouped into one or two dimensional arrays, they are able to
collect light of different wavelengths on different pixels or groups of pixels
simultaneously. In a double-beam instrument, the light is split into two beams
before it reaches the sample. One beam is used as the reference; the other beam
passes through the sample. The reference beam intensity is taken as 100%
Transmission (or zero Absorbance), and the measurement displayed is the ratio
of the two beam intensities. Some double-beam instruments have two detectors
(photodiodes), and the sample and reference beam are measured at the same
time. In other instruments, the two beams pass through a beam chopper, which
locks one beam at a time. Figure 3.14 shows the schematic diagram of UV-
visible spectrometer.
Figure 3.14 Schematic diagram of UV-VIS spectrophotometer
The detector alternates measuring between the sample beam and the
reference beam in synchronism with the chopper. There may also be one or
more dark intervals in the chopper cycle. In this case, the measured beam
intensities may be corrected by subtracting the intensity measured in the dark
interval before the ratio is taken. Samples are typically placed in a transparent
cell, known as a cuvette. Cuvettes are typically rectangular in shape, commonly
with an internal width of 1 cm. (This width becomes the path length, L, in the
Beer-Lambert law.) Test tubes can also be used as cuvettes in some instruments.
The type of sample container used must allow radiation to pass over the spectral
region of interest. The most widely applicable cuvettes are made of high quality
fused silica or quartz glass because these are transparent throughout the UV,
visible and near infrared regions. Glass and plastic cuvettes are also common,
although glass and most plastics absorb in the UV, which limits their usefulness
to visible wavelengths. Figure 3.15 shows the photograph of UV-Visible
spectrometer used to take the transmission and absorbance spectra.
Figure 3.15 Photograph of UV-Visible spectrophotometer
3.2.6 LCR Meter
Impedance measurements are a basic means of evaluating electronic
components and materials. Every material has a unique set of electrical
characteristics that are dependent on its dielectric or insulation properties.
Accurate measurements of these properties can provide valuable information to
ensure an intended application or maintain a proper manufacturing process.
When making these measurements, connection of the material to the measuring
instrument (an LCR Meter) is one of the major challenges faced, special fixtures
are generally required depending on the material type. The most common piece
of test equipment for holding a variety of solid materials is the LD-3, a liquid
tight, three terminal connection cell with electrode spacing adjustable by a
precision micrometer shown in Figure 3.16.
Figure 3.16 Photograph of Precision LCR Meter
Specimen Air
Cxm and Dxm Ca and Da
(a) (a) (b)
Figure 3.17 Schematic diagram of LCR measurement set up (a) with
specimen (b) without specimen
First the sample is inserted in the cell and the electrodes closed with the
micrometer until they just touch the sample lightly, Fig 3.17 (a). The
micrometer spacing hm is then recorded for this specimen. The capacitance
value, Cxm and dissipation factor, Dxm are then measured with the LCR meter.
The specimen is then removed from the cell, micrometer readjusted to and the
measurements repeated in air as Ca and Da, Figure 3.17(b).