k. ioakeimidi, t. maruyama, j.e. clendenin, a. brachmann stanford linear accelerator center
DESCRIPTION
Polarization comparison of InAlGaAs/GaAs superlattice photocathodes having low conduction band offset. K. Ioakeimidi, T. Maruyama, J.E. Clendenin, A. Brachmann Stanford Linear Accelerator Center Yu.A.Mamaev, L.G.Gerchikov, Yu.P.Yashin, D. Vasilyev St. Petersburg State Polytechnic University - PowerPoint PPT PresentationTRANSCRIPT
Polarization comparison of InAlGaAs/GaAs superlattice
photocathodes having low conduction band offset
K. Ioakeimidi, T. Maruyama, J.E. Clendenin, A. BrachmannStanford Linear Accelerator Center
Yu.A.Mamaev, L.G.Gerchikov, Yu.P.Yashin, D. Vasilyev
St. Petersburg State Polytechnic University V.M.Ustinov and A.E.Zhukov
Ioffe Physico-Technical Institute
R. Prepost University of Wisconsin
85-90%85-90%
Main depolarization mechanisms• Interband absorption
smearing due to bandedge fluctuations
• Hole scattering between HH and LH states causes a LH broadening
• Optical phonon scattering
• Non polarized electrons generated in the BBR
• Scattering of electrons in the BBR
Vacuum
electron6nm GaAs
100nm
Ec
HH1
Valence BandLH1
Ev
AlGaAs
Buffer
Conduction Band
BBR
HH- LH separation determined by well/barrier thickness and strainEC/EV determined by SL structure
Motivation for a flat Conduction Band structure• Observed emission spectrum
• Emitted electron polarization
dRYem
1
11
emS
S
SS
dPP
1
1
00 1
: optical absorptionR: reflection coefficient1: electron lifetime in BBRem: time of electron emission in vacuum P0: initial electron polarization upon excitation with circularly polarized lightS0: surface recombination velocityS : spin relaxation time in SLS1 : spin relaxation time in BBR
A. Subashiev et. al. SLAC-PUB 10901
Vacuumelectron6nm GaAs
100nm
AlGaAsBuffer Conduction Band
HH1
BBR
Valence BandLH1
Ev
Ec
Design of a flat conduction band structureStrained Barrier AlyInxGa1-x-yAs/GaAs SL on GaAs substrate
y: determines the bandgapx: lowers bandgap, controls EC and induces strain
EC(x,y)=QC1*Eg1(x)+QC2,def*(Eg2(y)+EC,def)Yu. A. Mamaev et al., PST2003
Unstrained wells and compressively strained barriers GaAs/AlyInxGa1-x-yAs SL
E vl2
E vh2
E c2
E v1
E c1
e1
lh1
hh1
Al0.21 In0.20 Ga 0.62 As
GaAs
8
6
Yu. A. Mamaev et al., Mainz 2004
dQW(Å) E hh2 E lh1 E hh1 E e1
10 -0.2054E+00 -0.1160E+00 -0.5120E-01 1.429 15 -0.1752E+00 -0.1041E+00 -0.4413E-01 1.429 20 -0.1542E+00 -0.9352E-01 -0.3794E-01 1.428 25 -0.1389E+00 -0.8409E-01 -0.3267E-01 1.428 40 -0.9484E-01 -0.6199E-01 -0.2145E-01 1.427
PhotocathodesSample # In % Al
%SL
Bandgap
eV
BBR doping cm-3
E(meV)
LH-
HH
EC
(meV)
meV)meV)
5506 17 18 1.449 1e19 52 19 15 20
5501 20 21 1.454 1e19 70 19 15 20
5503 23 25 1.469 1e19 68 10 15 20
5777 20 23 1.471 1e19 60 3 17 25
6329 20 22 1.463 7e18 61 11
6410 28 35 1.542 7e18 90 23
QW: 1.5nmQB: 4nmBBR: 6nmSL doping: 4e17cm-3
GaAsP/GaAs SL: 89meV LH-HH splitting EC=36meV, EV=19meV
650 700 750 800 850
10-2
10-1
100
QE SL-5506 27.09.2005 QE SL-5506 29.09.2005 Al
18In
17Ga
65As(4nm)-GaAs(1.5nm); ==15meV
Al18
In17
Ga65
As(4nm)-GaAs(1.5nm); ==15meV + BBR
QE,
%
wavelenght, nm
0
10
20
30
40
50
60
70
80
90
POL SL-5506 27.09.2005 POL SL-5506 29.09.2005 Al
18In
17Ga
65As(4nm)-GaAs(1.5nm); ==15meV; P*0.95
Al18
In17
Ga65
As(4nm)-GaAs(1.5nm); ==15meV + BBR
P, %
Green curve – without BBR absorption; Black curve – with BBR
#5506: In.17Al.18Ga.65As/GaAs SL
650 700 750 800 850
10-2
10-1
100
QE SL-5501 03.10.2005 QE SL-5501 04.10.2005 QE SL-5501 05.10.2005 QE SL-5501 06.10.2005 Al
21In
20Ga
59As(4nm)-GaAs(1.5nm); =15 meV =20meV
+BBR
QE,
%
wavelenght, nm
0
10
20
30
40
50
60
70
80
90
100
POL SL-5501 03.10.2005 POL SL-5501 04.10.2005 POL SL-5501 05.10.2005 POL SL-5501 06.10.2005 Al
21In
20Ga
59As(4nm)-GaAs(1.5nm); =15 meV =20meV; P*0.95
Al21
In20
Ga59
As(4nm)-GaAs(1.5nm); =15 meV =20meV; P*0.95+BBR
P, %
Green curve – without BBR absorption; Orange curve – with BBR
#5501: In.20Al.21Ga.59As/GaAs SL
650 700 750 800 850
10-3
10-2
10-1
100
QE SL-5503 21.09.2005 QE SL-5503 22.09.2005 QE SL-5503 23.09.2005 Al
25In
23Ga
52As(4nm)-GaAs(1.5nm); ==30meV
Al23
In23
Ga54
As(4nm)-GaAs(1.5nm); ==30meV Al
25In
23Ga
52As(4nm)-GaAs(1.5nm); ==30meV; + BBR
QE
, %
wavelenght, nm
0
10
20
30
40
50
60
70
80
90
POL SL-5503 21.09.2005 POL SL-5503 22.09.2005 POL SL-5503 23.09.2005 Al
25In
23Ga
52As(4nm)-GaAs(1.5nm); ==30meV; P*0.90
Al23
In23
Ga54
As(4nm)-GaAs(1.5nm); ==30meV; P*0.90 Al
25In
23Ga
52As(4nm)-GaAs(1.5nm); ==30meV; P*0.95 + BBR
P, %
Green curve – In0.23Al0.25Ga0.54As – 1.5 nm GaAs without BBR absorption
Blue curve – , In0.23Al0.23Ga0.54As – 1.5 nm GaAs without BBR absorption; Black curve – In0.23Al0.23Ga0.54As – 1.5 nm GaAs with BBR
#5503: In.23Al.25Ga.52As/GaAs SL
1.4 1.5 1.6 1.7 1.8 1.9
20
40
60
80
100
Pol
ariz
atio
n, %
Photon energy, eV
Experiment SL 5-777 Theory In
20Al
23GaAs(40)/GaAs(15)*0.95, =25, =17meV
Theory In20
Al23
GaAs(36)/GaAs(15)*0.95, =25, =17meV
#5777: In.20Al.23Ga.59As/GaAs SL
92%
Simulations vs data analysis• Data indicates a blue shift for the polarization peak for
samples 5501, 5503, 5506
• In theory longer wavelengths give higher polarization because they obey better the selection rules
• In practice longer wavelengths photogenerate electrons primarily in the BBR where there is no polarization selectivity and also
• the electrons photogenerated in the SL structure in this case thermalize more in the BBR and they have lower tunneling probabilities due to tighter confinement and due to the CB peak at the interface between the SL and the BBR.
#6329: In.20Al.22Ga.58As/GaAs SL
85
80
75
70
65
60Po
lari
zati
on (
%)
860850840830820
Wavelength (nm)
St. P 520 C 540 C 540 C
St. Petersburg 78%CTS 76 ~ 77%
850800750700650
Wavelength (nm)
80
60
40
20
Pola
riza
tion
(%
)
St. P CTS
#6410: In.28Al.35Ga.37As/GaAs SL
80
60
40
20
Pola
riza
tion
(%
)
800780760740720700680660
Wavelength (nm)
St. P CTS
85
80
75
70
65
60
Pola
riza
tion
(%
)
800795790785780
Wavelength (nm)
St. P CTS 1st activation CTS 2nd activation
St. Petersburg 74%CTS 77%
(004) X-ray
Indium fraction (assume 100% strain): 5-777 19.6% 5501 20.7%
Superlattice thickness: 5-777 5.01 nm 5501 5.10 nm
5-777 is better
(004) simulation
10-8
10-7
10-6
10-5
10-4
10-3
10-2
10-1
-2.0 -1.5 -1.0 -0.5 0.0 0.5 1.0 1.5
(deg.)
0
+1
SimulationI n0.20Al0.21Ga0.59As (4 nm) - GaAs (1.5 nm)Assume 100% strain
Summary of Polarization Results
Sample # In % Al% Polarization %
5506 17 18 82-85
5501 20 21 84-90
5503 23 25 75-82
5777 20 23 92
6329 20 22 76-78
6410 28 35 75-82
How can we explain 90%?• Polarization calibration seems OK
within 2-3%.• 5-777 had an As-cap, allowing a
low temp heat-cleaning.• When 5-777 was heated to >540 C,
polarization dropped to 84%, which is consistent with SVT-5501.
• Surface effect supported by the temperature of the heat cleaning dependence of the results
• X ray shows decreased barrier size that would imply higher strain
• Strained barrier structures do not preserve strain in the BBR; we think that 5777 might have reduced BBR thickness.
Conclusions• The flat CB structures show promising polarization
results with a record polarization of 92%.
• Further analysis needs to be done in order to understand depolarization effects primarily in the BBR.
• The flat CB photocathodes show sensitivity to heat cleaning temperature. The heat cleaning effect needs to be explored further with SIMS analysis.
More SVT results
80
70
60
50
40
30
20
Pola
riza
tion
(%
)
850800750700650
Wavelength (nm)
0.001
0.01
0.1
QE (%
)
80
70
60
50
40
30
20
10
Pola
riza
tion
(%
)
850800750700650
Wavelength (nm)
2
3
4
5
678
0.1
2
3
4
5
678
1
QE (%
)
SVT-5503 SVT-5506
SVT-5501 (5-777 duplicate)
2
3
4
5
678
0.1
2
3
4
5
678
1
2
QE (%
)850800750700650
Wavelength (nm)
80
60
40
20
Pola
riza
tion
(%
)
95
90
85
80
75
70
65
60
Pola
riza
tion
(%
)
850845840835830825820
Wavelength (nm)
1st activation 500 C 24 hr af ter 1st activation 2nd activation 500 C 3rd activation 540 C
Peak polarization ~84%
Dear Takashi,
We have analyzed your recent data on SL-5501-5506 and agree with your conclusion that the polarization losses could be due to the surface effect. To confirm this assumption we compare your experimental data (points) with our calculations (curves - see figures below).
First we calculate the initial polarization of photoelectrons in the working layer using your data of layer composition and thickness.
Then we reduce the resulting polarization of emitted electrons by 5% due to the polarization losses in the surface region (. “Energy resolved spin-polarized electron photoemission from strained GaAs/GaAsP heterostructure”, Yu.A.Mamaev, A.V.Subashiev, Yu.P.Yashin, H.-J.Drouhin and G.Lampel, Solid State Comm., Vol. 114, No 7, 2000, pp 401-405.).
We have reasonable agreement between the theory and experiment for the overall behavior of polarization spectra for SL 5501 and 5506. For SL 5503 the agreement can be achieved if we assume that the actual Al concentration in barrier layer is 2% lower, i.e. SL 5503 4 nm In0.23Al0.23Ga0.56As – 1.5 nm GaAs.
However there is a systematical discrepancy between the theory and experiment in the region of polarization maximum, namely experimental peak is blue shifted and smaller in amplitude. In our calculations the position of the polarization maximum is close to the photoabsorption edge. The QY spectrum behavior near the edge evidences that the position of photoabsorption edge is calculated correctly. Thus the observed blue shift of polarization maximum and large polarization losses might be caused by an additional physical reason.
We assume that this effect can arise from the photoabsorption in the surface (BBR) layer (see our last joint paperA. V. Subashiev, L. G. Gerchikov, Yu. A. Mamaev, Yu. P. Yashin, J. S. Roberts, D.-A. Luh, T. Maruyama, and J. E. Clendenin “Strain-Compensated AlInGaAs-GaAsP Superlattices for Highly-Polarized Electron Emission”, Appl. Phys. Lett. 86 (2005) 171911). In figures below we show the polarization spectra accounting for the BBR contribution to electron emission. Figures demonstrate that this contribution cuts the red side of the polarization maximum resulting in its sizable blue shift and decreasing of amplitude.
The similar effect we also observe in SL 6-329 and 6-410. However it seems that in our best sample, SL 5-777, there is no visible BBR contribution. In the last figure we show the polarization spectrum of SL 5-777 together with our calculations. We use the latest Ioffe PTI data on its composition. According to this data SL 5-777 is 3.6 nm In0.20Al0.23Ga0.57As – 1.5 nm GaAs. The barrier thickness we reduce by 0.4nm according to X-ray results, though this change does not almost affect the polarization spectrum. Figure show that our calculations without BBR contribution (initial polarization – 5% surface losses) reproduce well the experimental spectrum. Unfortunately we do not understand at the moment why some samples are good and some samples with close or even the same design are bad.
Vacuum
electron6nm GaAs
100nm
Ec
HH1
Valence Band
LH1
E v
AlGaAs
Buffer Conduction BandBBR
InAlGaAs-GaAs superlattice
• St. Petersburg group observed 90% polarization from InAlGaAs-GaAs superlattice (5-777).
• SVT grew three wafers– 5506: 4 nm In0.17Al0.18Ga0.59As – 1.5 nm GaAs 18 periods– 5501: 4 nm In0.20Al0.21Ga0.59As – 1.5 nm GaAs 18 periods (duplicate of 5-777)– 5503: 4 nm In0.23Al0.25Ga0.59As – 1.5 nm GaAs 18 periods
• Peak polarization of SVT-5501 was 84%.• Three samples from St. Petersburg
– 5-777 Could not activate to high enough QE. No measurements.– 6-329 4 nm In0.2Al0.22Ga0.58As – 1.5 nm GaAs 18.5 periods
– 6-410 3.07 nm In0.28Al0.354Ga0.366As – 0.56 nm GaAs 15 periods
• X-ray diffraction of Ioffe 5-777 and SVT-5501