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Journal of Non-Crystalline Solids 137&138 (1991) 543-546 North-Holland
JOURNAL OF
NON-CRYSTALLINE SOLIDS
THE MECHANISM OF SUBNANOSECOND CARRIER RECOMBINATION IN a-Sl:H
R. VANDERHAGHENol, A. MOURCHID(II(z) ,D. HULIN{Z),D. A. YOUNGer, W. L. NIGHAN Jro), P.M. FAUCHET(~)
1 Laboratoire de Physique des Interfaces et Couches Minces (UPRA 258 du CNRS) Ecole Polytechnique, 91128 PALAISEAU Cedex FRANCE
2 Laboratoire d'Optique Appliqu~e (URA 1046 du CNRS) ENSTA-Ecole Polytechnique, 91120 PALAISEAU FRANCE
3 Laboratory for Laser Energetics, University of Rochester, ROCHESTER N.Y.14623 USA 4 Department of Electrical Engineering Princeton University, PRINCETON N.J.08544 USA
We report on the non-radiative picosecond recombination of photogenerated ( free or trapped) carriers in a- Si:H and alloys. The mechanism is bimolecular multiphonon, with a limited number of recombining states. The recombination efficiency of tail states is discussed.
1. INTRODUCTION
This paper reports our investigation of ultrafast
trapping and recombination of carriers in a-Si:H
and alloys. We use the techniques of femtosecond
pump-probe spectroscopy 1. An ultrashort laser
pump pulse, at 2 eV (or 1.4 eV), photoexcites a
density of free (or trapped) carriers N. A probe pulse
tests the resulting photoinduced change in the
optical properties at various time delays.
2. EXPERIMENTAL ARRANGEMENT
The ultrashort optical pulses are generated from
a colliding pulse mode-locked dye laser and
amplifier system, producing pulses of tunable
wavelength, with less than 100 fs in duration and at
a repetition rate of 20 Hz. The pump beam, at 0.62 #m (2 eV), is focused to a diameter of 1 mm. Free
carriers are injected above the mobility edge of the
sample (the measured gap for a-Si:H is 1.7 eV on a
Tauc plot), with a carrier density ranging from more than 1019 tO less than 1021 cm -3. The technique of
self phase modulation is used to generate a white
light continuum. A fraction of this beam is selected in the infrared spectrum at 0.88 #m, amplified in a
three stages IR dye amplifier, and can be also used
as a pump 2 to inject trapped carriers. The other
fraction of the continuum is selected with
interference filters and used as a probe beam.
The undoped a-Si:H and the alloys with C or Ge
are deposited on silica and their thickness is less
than one absorption length at 2 eV. They have been
prepared by rf glow discharge, with a deposition
rate of 1 ,&,/s and a substrate temperature of 230 °C.
We measure the absolute change in reflection
and transmission of the probe pulse as a function of
time delay with respect to the pump pulse. For each
delay point, the complex index of refraction, n + ik,
is calculated using the "thin absorbing film"
equations. This directly provides the induced
change in real refractive index (An) and the photoinduced absorption (Acz = 4~Ak/X). These
quantities are measured at least at two probe wavelengths, 1 lam where Ak is only sensitive to the
carriers, and 0.52 #m where there is a
superposition of carrier effect and lattice heating 3.
3. CARRIER DYNAMICS
We have shown previously that both electronic
and thermal effects induce transient changes in the
real and imaginary parts of the index. The
electronic contribution results from intraband absorption with an effective cross-section o. The
short wavelength probes are sensitive also to
thermal effects through the increase of interband
absorption which follows thermal band gap
0022-3093/91/$03.50 © 1991 - Elsevier Science Publishers B.V. All rights reserved.
546 R. Vanderhagen et aL /Mechanism of subnanosecond carrier recombination ih a-Si:H
density, where this mechanism is the most efficient,
the mean excess energy of the remaining carriers
should be around 1 eV. Taking into account the
measured 5 1 eV/ps thermalization time, there
should be a 1 ps delay between recombination and
lattice heating, which is incompatible with the 100 fs
upper limit 2 for the delay between recombination
and complete lattice heating. We thus attribute this
bimolecular recombination to a mutiphonon
mechanism. The recombination efficiency is the
same for free carriers and for trapped carriers at
least 100 meV below the band edge, but it is
reduced for carriers in deep traps : at very low carrier density, we observe a residual Ak which
depends on the sample decreases very slowly and
cannot be attributed to a thermal effect. The saturation value of '~eff measured at very
high N excludes a recombination process between
hot carriers. At least one carrier needs to be cold (in
a limited number of states near the band edge) or
trapped at the top of the band tail.
When the carriers are directly generated in the
band tail within 100 meV of the extended states
(with the IR pump in a-Si:H or the 2 eV pump in a-
Si:C:H), the recombination can be fitted with the
same parameters as when the carriers are in the
extended states in a-Si:H. Therefore, carriers in
these traps, are as efficient for recombination as
when they are in the extended states
The nearly constant 'teff(Ak) at low N could be
attributed either to ~ or to recombination. However,it
is observed as well at t = 0 + and at longer time.; moreover, Ak decreases roughly exponentially over
one order of magnitude. We then attribute it to
bigger recombination efficiency of a limited number
of tail states.
7. CONCLUSIONS
We have observed, for a-Si:H and its alloys, a
bimolecular multiphonon recombination of carriers
in the extended states or in the band tail states. This
recombination involves one cold or trapped carrier.
Carriers trapped at the top of the band tai l , at least
down to 100 meV below the edge, exhibit the same
recombination efficiency. Some from these tail traps
are more efficient for recombination, and deeper
traps are less efficient. Finally, the observed
recombination cannot be an Auger type.
ACKNOWLEDGEMENTS
The work at Rochester is supported by ONR
(N00014-91-J-1139) and NSF (ECS-9196000).
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