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A REVIEW ON THERMAL DONORS IN CZ-SILICON AND THEIR
IMPACT ON ELECTRONIC INDUSTRY
Rajeev Singh
Asst. Professor, Department of Physics, Arignar Anna Government Arts & Science College, Karaikal (UT of Puducherry) -609605, India
P. B. Nagabalasubramanian
Asst. Professor, Department of Physics, Arignar Anna Government Arts & Science College, Karaikal (UT of Puducherry) -609605, India
Abstract
CZ-silicon is the primary material for integration of many
electronic components since 1960 after the replacement of
Germanium. Many impurities are inbuilt in the crystal.
Among these, presence of Oxygen & Nitrogen prominently
affects the electrical and optical properties. In this article, an
attempt has been made to discuss about oxygen related
donors, their identification and kinetics of formation. We
will also try to project the positives and negatives related to
the problem in particular relating to electronic industry and
its future prospects.
Keywords: CZ-silicon, Thermal donors, Oxygen
Need of hour
Silicon is mostly used material in Integrated Chips and Solar
panels manufacturing. In the present era, it is essentially
required to increase the number of circuits in a single chip
and thereafter the number of operations in them. For
reducing the packaging cost and failure rate of chips, the
heat generation must be lower. In power devices, the
excessive leakage current can be produced due to defects
below the surface. The interstitial type dislocation loops in
the active regions of the devices may cause degradation of
minority carrier lifetime, alter diffusion profiles and may
shift p-n junction characteristics [1-3]. In very lightly doped
silicon, these oxygen related thermal donors (TDs) can
modify the resistivity of material and hence they can affects
numerous resistivity-dependent device parameters. The
oxide precipitates present in the active region may increase
the leakage currents in the p-n junctions; reduce refresh
times in DRAM memories etc [4]. The proper
characterization and understanding regarding the role of
oxygen related impurities is essential to optimize the yield.
Comparison and importance of silicon over other
semiconductors
Many other semiconductors and their compounds have been
examined as a replacement of silicon e.g. GaAs, InP etc.
GaAshas certain technical advantages over silicon. Due to
higher bandgap energies and motilities,GaAs power
amplifiers have higher gain even at lower operating voltages.
Its band gap can be varied also with inserting one type of
atoms, i.e. GaAlAs, GaInP etc. Since GaAs has direct band
gap so it is also convenient for Laser &optoelectronics [5].
The device components of GaAs generate less noise than
silicon and most other types of semiconductor components
and hence they are useful in weak-signal amplification
applications. There are some drawbacks also in GaAs e.g.
the out diffusion of As at high temperatures, adjustment of
the threshold voltage etc [6]. The thermal conductivity of
GaAs is about three times lower than that of silicon. Silicon
is roughly a thousand times cheaper than germanium, i.e. the
cost of 8 inch diameter silicon wafer is around $ 5 but for
GaAs is around $ 5000/. Therefore, GaAs devices are only
used in specific applications where their special capabilities
justify their higher cost. However, some researchers in
Stanford University are working to prepare the lower cost
chips of GaAs [7].
Production of silicon single crystal
Single crystals of silicon are produced primarily by
Czochralski (CZ) method [Fig.1]. However, for power
devices, Salnick et al developed a new growth techniqueto
grow untraditionally doped CZ-grown silicon [8]. The other
method is Float Zone (FZ) method. FZ – Si is very soft for
most commercial applications and crumbles very easily
because it contains over two to three orders of magnitude
less oxygen than Cz-Si. The oxygen precipitates helps to
suppress stacking faults. Presence of oxygen makes the Si
more resistant to thermal stress during processing [9].
Therefore, CZ-Si is used for integrated circuit designs
having many thermal processing steps.
In Czochralski method, the polycrystalline silicon is melted
in a silica crucible heated by a resistor or by RF currents
[Fig 1]. Under steady conditions and after stabilizing the
melt flow, the seed is lowered towards the melt. Now, the
crystal and the crucible rotate in opposite directions. After
dipping the seed into the melt, a stable interfere between
melt and seed crystal is adjusted [2] and a large amount of
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oxygen from crucible is incorporated in to the melt. Oxygen
is acting as a gettering agent so it promotes the internal
gettering process. However, a certain level of oxygen
concentration is quite essential for mechanical strength of
the wafer. Many types of impurities are found in crystal melt.
The impurity concentration in the solid part CS differs from
the concentration CL in the liquid part just at the interface.
The ratio of Cs to CL is called segregation coefficient ‘k’
and it has different values for different materials in which
oxygen has the value 1.3 greater than all other types of
impurities [6]. Now, the seed is crystallized after pulling
from the melt upward at the solid-liquid interface [2]. In this
process, the seed must be not touched to the melt surface to
avoid the generation of dislocations due to thermal shock.
Therefore, the process of necking is performed for
dislocations free growth.
Fig.1: CZ-Si growth (1) Silica crucible, (2) carbon suscepter,
(3) Graphite heater, (4) Single crystal Silicon.
Review of research and development in the subject
Oxygen, the most common impurity, is being introduced
from the crucible during the early stages of growth of the
crystal. Its behavior is different under lower and higher
temperatures annealing. The annealing at round 450o C leads
to a change of its material’s electrical resistivity. Upon heat
treatments, the oxygen impurities in silicon interact with
other defects already present in the crystal. These oxygen
atoms in interstitial sites are electrically inactive but they
create, upon low temperature annealing, high concentrations
of electrically active centers [10]. These centers were
discovered by Fuller et al in 1954. They were called as
Thermal Double Donors or Thermal Donors. The types of
oxygen donors are given in the table [10-12].
Kaiser et al reported the oxygen related thermal donor
formation kinetics with dependence of interstitial
concentrations and a model known as KFR model was given
by them in which only three complexes of Si with 2-4
oxygen atoms are electrically active [13]. Wada and Inoue
[14] modified this model by considering electron emission.
Table: Oxygen related Donors with their generation temperature
S.
No.
Type of
Oxygen
donors
Annealing
Temperature
Annealing
Time Reference
1 Thermal
donor (TD) 300-500°C <105 min
Fuller et al.
(1954) [10]
2 New donor
(ND) 550-800°C <105 min
Kanamori and
Kanamori
(1979) [11]
3
New thermal
donor
(NTD)
450-550°C >105 min
Kamiura et
al. (1990)
[12]
In OSB model [15] Si atom at the center and surrounded by
five or more oxygen atoms give birth to donor activity. In
another model by Mathiot [16], three oxygen atoms with
one or more atoms in interstitial position form thermal
donors. McQuaid et al [17] proposed that oxygen loss
during low temperature anneals followed second order
kinetics. At higher temperature (T > 450 oC), the rate of the
loss of oxygen concentration were less than expected rate of
(Oi-Oi) interaction and tended to vary with increasingly high
powers of oxygen concentration [18]. Murin et al [18] had
also investigated the Radiation induced complexes of
oxygen, carbon, vacancy and interstitials in silicon by
absorption spectroscopy. According to Newman et al, TD (n)
centers have only a few oxygen atoms clustered together
[19-21]. They proposed that oxygen dimers O-O may
diffuse more rapidly than isolated oxygen atoms [21].
Aforesaid workers and many others have tried to look into
the problem of oxygen related donors (ODs) from different
angles and contributed reasonably in order to evolve a
widely accepted common consensus for the proper
understanding of the exact mechanism [22].
Ono et al. [23] have studied anomalous ring-shaped
distributions of oxygen precipitates in wafers using infrared
absorption spectroscopy and X-ray topography. FTIR
measurements showed homogenous distributions of oxygen
precipitates, interstitial oxygen and thermal donors. The
results also showed that the thermal donors and interstitial
silicon atoms in the wafers do not affect oxygen
precipitation. Therefore, Ono concludes that native point
defects, impurities or their clusters in as grown wafers are
not responsible for inhomogeneous precipitation after
thermal annealing. The anomalous distributions should be
strongly affected by already existing precipitates except
OSF nuclei. The density of OSF nuclei, which were also
heterogeneously nucleated at high temperatures during
crystal growth, is too low to directly affect the
inhomogeneous precipitation.
Capaz et al [24] identified the process of enhanced oxygen
diffusion due to interaction between interstitial oxygen and
hydrogen atoms. This interaction is also supported by IR
absorption following an annealing after implantation of
hydrogen atoms into Silicon [25-26]. Newman [27] has very
beautifully presented an overall scenario of past and present
state of art clearly indicating that the processes involved
therein are not yet fully understood.
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The behavior of Oi in the presence of N is not yet fully
understood. It exhibits electrically inactive NNO defect.
Many N/O experiments have been suggested for our
understanding of how the nitrogen atoms diffuse, and form
the complexes with either interstitials or with dimers [28-30].
The hydrogen passivation and carbon suppression of thermal
donors have also been studied [31]. Yang et al [32-33] have
beautifully tried to look into the behavior of STDs in silicon
doped with isotopic oxygen and also grown-in defects in
nitrogen-doped CZ-Silicon. Some results on electrical
properties of H implanted Si annealed under high
hydrostatic pressure have been reported by Kaniewska and
Misiuk [34]. We have been consistently pursing the research
work [35].
Till now, sixteen neutral (TDD1-TDD16) and nine
positively charged species (TDD1-TDD9) of thermal double
donors have been detected and confirmed through infra-red
absorption spectra [36]. M. Pesola et al gave the
confirmation about the structures of TDD0, TDD1 to TDD7
on the basis of accurate total energy calculations and made a
good agreement with Chadi [37-38]. The other possible
structures for all the TDDs and the most probable average
number of oxygen atoms involved in a single TDD has been
given by us [39].
Measurement & Techniques
There are many techniques for detection and measurement
of donors such as Hall Effect, Four probes, FTIR, DLTS,
XRD, PL etc. Here we are giving only a brief introduction
about the resistivity measurement and FTIR.
(a) Resistivity
The resistivity of unannealed/annealed Si samples will
be measured with the help of most commonly used
collinear four-probe method the number of carriers are
determined with the help of Irvin’s curve [40]. To
ascertain the carrier concentration, the results are also
be supplemented by Hall measurements.
(b) Donor Generation
After receiving the desired heat treatment in air or
nitrogen ambient, the samples are cleaned in
hydrofluoric acid in order to eliminate the surface oxide.
Now by measuring its new resistivity, the
corresponding number of carriers is again obtained
from Irvin’s curves [40]. We can deduce the number of
donors generated or eliminated during the given heat
treatment by calculating the difference of number of
carriers with the approximation that the mobility
remains constant.
(c) FTIR Spectroscopy
FTIR measurements will be used for determination of
the oxygen and carbon absorption coefficients at room
temperature from 3500 cm-1 to 600 cm-1 band
respectively enabling us, to know about the
reduction/precipitation of oxygen/carbon contents in the
annealed/unannealed samples. TD (n), where ‘n’ ranges
from 0 to 16, may also be identified through FTIR
spectra.
(d) Precipitated oxygen and carbon concentration
These concentrations are measured initially in the wafers
received as such. Then again the concentrations of Oi
and Cs were determined after the scheduled heat
treatment. The difference between these concentrations
of annealed and unannealed samples helps to find the
precipitated oxygen and carbon during heat treatment of
samples.
(e) Activation energy of thermal donors
In the low temperature annealing (< 500 oC), the rate of
loss of interstitial oxygen atoms (Oi) may be related by
trapping with other such atoms [41]. Assuming that
backward reaction rate is negligible in comparison to the
forward reaction rate, the kinetics of Oi loss would be
controlled solely by the interaction rate of two randomly
diffusing Oi atoms [42].
2[ ]8 [ ]i
id O DR O
dt
Where R = radius of capture associated with dimer
formation, D = Diffusion coefficient for oxygen
Now, integrating the above expression,
1 18
[ ] [ ]i i i o
DRtO O
or1 1( ) ( ) 8C t C O DRt
where1 1( ) and ( )C t C O
are reciprocal values of
oxygen concentration prior to the anneal and after
anneals for time ‘t’. Plot of [1 1( ) ( )C t C O ] versus
time is expected to be linear having the gradient equal
to8 DR . Then, we can get the value of diffusivity of
oxygen for a particular temperature. Now, the value of D
so obtained is substituted in the expression
0.17exp /D E kT cm-2s-1. Hence, the value of
activation energy for the diffusion of oxygen can be
calculated [42]. We can find the formation of donors
species at different temperature for different annealing
time.
Conclusion
In spite of more than sixty years of research about thermal
donors, many fundamental questions are unanswered
regarding their structures and their method of formation.
Some of them are as follows:
What are the exact structures and formation processes
for different types of thermal double donors?
How many types of donors can exist?
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What is the role of silicon interstitials in the formation
of TDDs? They are part of defect structures or they are
working as a catalyst for defect formation.
What is the role of oxygen dimers?
The high temperature (T > 700 oC) anneals are well
understood now a days. But, the lower temperature
processing is still a matter of debate. It is strongly needed to
improve the understanding about this because the device
processing temperatures and the size of future devices are
decreasing continuously.
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