Cu(In,Ga)(S,Se)2 Crystal Growth, Structure, and...
Transcript of Cu(In,Ga)(S,Se)2 Crystal Growth, Structure, and...
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College of Engineering University of Illinois
Cu(In,Ga)(S,Se)2 Crystal Growth, Structure, and Properties
Angus RockettDepartment of Materials Science
The University of Illinois1101 W. Springfield Avenue,
Urbana, IL 61801, USA217-333-0417 [email protected]
With support from:
The National Renewable Energy Laboratory
mailto:[email protected]
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College of Engineering University of Illinois
CIGS
• Chalcopyrites have been proposed as spin-polarized electron emitters.
• They are also interesting for other applications including thin film transistors.
• Primary application -- solar cells
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Useful Properties• Engineerable energy gap in useful range
(< 1eV to >2 eV).
• Very high optical absorption coefficient.
• Usable as polycrystals.
• Native defects “harmless” (all shallow).
• Few observable problems with impurities.
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Basic crystallography and thermodynamics
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Disordering energy is low so there are many point defects
A polar compound socharged surfaces could
be a problem c
a
Cu
In or Ga
S or Se
c/2a ratio varies from >1 (high In) to
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Chalcopyrite Cu(In,Ga)(S,Se)2
Polar
Metal
Metal
Chalcogen
Chalcogen
Polar
Non-polar
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Ternary Phase Diagram…and right away we know we are in trouble.
Cu2SeIn2Se3
CuInSe3
Pseudobinary…is valence compensating
What is observed:
γ: CuIn5Se8
β: ~CuIn3Se5
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Pseudobinary Phase Diagram
Note: extended solubility in αphase.
Low-temperature chalcopyrite-sphalerite transition suggests low cation ordering energy.
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Deposition Methods
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Evaporation
• Multisource Evaporation •• High rateHigh rate•• Easy controlEasy control•• Difficult to scaleDifficult to scale•• High temperature High temperature
processprocess
Most epitaxy by MBEMost solar cells this way
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+Se
Selenization• Deposit metals separately• React with a Se source (Se vapor or H2Se). • Similar processes with sulfides• Sequential, easy to control• High film stress• Reaction of metal layers & phases formed are critical,
processes complex.
Heating lamps
Metal sources
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MOCVD
ScrubberPumps
Valve
LoadLock
Reactor
BufferVolume
ComputerControl
Flow Controllers & Vents
Source Gases
Safety Enclosure
Toxic GasAlarm System
Hydrogen selenideTrimethyl Ga or trimethyl InComplex Cu compound: use bubbler source. Low rate.
Best growth:Cu-rich films500-550°C
Epitaxy by MOCVDat Hahn Meitner Institute
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Growth rate ~ 1µm/hr.Substrate temperature: 550-725°C
Cu-Ga target for Cu(In,Ga)Se2Cu target for pure CuInSe2Cu and Ga targets for CuGaSe2
Typical hole mobility ~280 cm2/V-sec
Typ. Carrier Lifetime: ~ 0.4 nsec
Hybrid MethodGrowth Process:• Similar to MBE• Evaporate Se• Sputter metals• Optional rf coil for
ionization
Epitaxy on GaAs:
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Band Structure
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Band Structure - TheorySe-S alloys mostly affect valence band edge.
In-Ga alloys mostly affect conduction band.
Cu-Ag alloys have minor effects on both bands.
Gaps are low because of Se-p : Cu-d repulsion.
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Experimental UPS• Se capped surface (112)Se cleaned
thermally shows Ef - EV ~ 0.47 eV.
• Agrees well with data from other labs
Cu 3d
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Optoelectronic Properties
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Photoluminescence Data
Data: S. Siebentritt et.al.Hahn Meitner Institute
Cu-rich films show sharp emissions:
Donor-acceptor emissionsWeak band-band emission
Group-III rich films show broad emissions.
Polycrystals same as epilayers
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Photoluminescence Lifetime
10
100
1000
10000
100000
0.E+00 1.E-09 2.E-09 3.E-09 4.E-09 5.E-09 6.E-09
NRELSSIGSEEPVISETUI261BUI261AUI291UI286
Lifetimes 0.2-4 nsec
Consistent with direct-gap band structure
Microsecond decay (not shown shows deep state)
Epilayers have short lifetimes. Suggests minority carrier traps.
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Defect-to-defect, not band-to-band recombination.
Photon energy does not track the gap change withGa.
Similar to CIS PL data. 1
10
100
1000
104
900 1000 1100 1200 1300 1400 1500Em
issi
on In
tens
ity (A
rb. U
nits
)
Wavelength (Å)
Red: 283 KYellow: 238 KBlue: 171 KPurple: 110 K
IncreasingCurrent
At least 4 fixed peaks
Electroluminescence
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Defect 1 Defect 2 Defect 1 Defect 2Energy above VBE 0.8 0.9 0.8 1 E(gap) 1.22Width 0.13 0.15 0.13 0.15 Band Tail width 0.022Concentration 1.00E+14 3.50E+14 1.00E+14 1.10E+15 Band Tail DOS 1.00E+18
IEC Device UIUC Epilayer DeviceBoth Layers
Experimental Data for deep levels
Thermophotocapacitance Cathodoluminescence
1E+12
1E+13
1E+14
1E+15
1E+16
1E+17
1E+18
0.5 0.8 1.1 1.4Energy Above Valence Band (eV)
Fit based on data from Temperature Photocapacitance(J. Heath and D. Cohen, U. Orgegon)
Quantitative estimate of defect state densities.
Subgap states produce clear CL emission spectra
Data from Y. Strzhemechny and L.Brillson, Ohio State U.
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101210131014101510161017101810191020
0 10 20 30 40 50
Hol
e C
once
ntra
tion
(cm
-3)
1000/T [K-1]
300 100 50 30 20Temperature, T [K]
CIGS x=.20CIGS x=.56
CIGS x=.11
CGS, x=1.00
Carrier Concentration: Hole Mobility:
100
1000
10 100Temperature, T [K]
Hol
e M
obilit
y (c
m2 /V
s)
Hall Effect
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No change in electrically-active defects with Cu/III composition.
10121013101410151016101710181019
0.9 0.95 1 1.1 1.1 1.1 1.2
Stat
e C
once
ntra
tion
(cm
-3)
Cu/In Ratio0.7 0.75 0.8 0.85 0.9 0.95 1
Cu/(In+Ga) Ratio
NA1NA2ND
10121013101410151016101710181019
Hall Effect -- vs. composition
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101410151016101710181019102010211022
0 0.2 0.4 0.6 0.8 1
Acce
ptor
Sta
te D
ensi
ty [c
m-3
]
Ga/(In+Ga)
…except for Ga, which increases p at high Ga contents.
Open points: Ga gradientClosed points: uniform Ga
Hall-effect -- vs. composition
Deep acceptor (135 meV)
Shallow acceptor (40 meV)
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• (112) and (002) very similar, phonon scattering for (112) and (002)• p (220) 20x lower, mobility lower, defect limited
10
100
1000
100 150 200 250 300Temperature, T (K)
Hal
l Mob
ility
(cm
2 /V-s
ec)
Film Orientation(112)(002)(220)
3 3.5 4 4.5 5 5.5 6 6.5 7
Inverse Temperature, 1000/T [K-1]
Hol
e C
once
ntra
tion,
p (c
m-3
)
1017
1016
1015
1014
1013
Growth Orientation Effects
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Low dose Se implant -- mostly reversible changes.
70 80 100 2000.1
1
10
100
1000
Mob
ility,
µ (c
m2 /V
s)
Temperature T (K)300
as depositedas implantedannealed
1011
1013
1015
1017
1019
2 4 6 8 10 12
Hol
e C
once
ntra
tion
(cm
-3)
1000/T (K )
Implantdamage Implant
damage
Implant Changes
Cr implant similar
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Point Defects Summary
Conduction Band
Valence Band0.
9 eV
0.7
eV
0.3
0.130.04Ef
CuIn-2
CuIn-1
VCu-1
InCu+1 or Vse+1 ?InCu+2 or Vse+2 ?
• Shallow acceptor: Cu vacancy
• Deep acceptor: CuIn (divalent)
• Defects 0.8 and 1.0 eV above valence band: probably Se vacancy
• Above do not shift with Ga/(In+Ga)
• Additional deep states?
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Surface Energy & Growth Mechanisms
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Surface MorphologySummary:Best epitaxy on GaAs (111). Rough surfaces on GaAs (110).
Epitaxial temperatures:
Ts = 540 ° C (220); 640 ° C (100); and 700 ° C (112)
Pure CuInSe2:
Ga diffuses from the substrate
Kirkendall voids form at the interface in the GaAs substrate.
(100)/(002) surfaceElongated ripples with asymmetric rectangular pits sometimes present.
(220)/(204) surfaceFacets to (112) planes, one smooth, one rough.
(112) close-packedVery low angle (
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(112)Se Close Packed Surface
Very triangular facets, strong step orientation
5 5 µµm x 5 m x 5 µµm AFM imagem AFM image
Steps: 1-3 ML high• Growth by step nucleation and
propagation
• Very flat
• 180° growth twins ~40 µm apart
Electron Channeling Patterns
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(112)Metal Close Packed SurfaceSteps: 1-2 ML high
• Growth by step nucleation and propagation
• Very flat
• No growth twins over the entire surface!
Very triangular facets, strong step orientation
5 5 µµm x 5 m x 5 µµm AFM imagem AFM image
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(112) Surface Steps Compared• Both surfaces show triangular pyramids -- very similar
Metal-terminatedSe-terminated
One type of step dominatesMore preference on Se-terminated surface
Inside corners!
Layers nucleate near terrace
edges!
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Implications for Steps
Island Perimeter
3 edges with onedangling bond per edge atom
3 edges with two dangling bonds per edge atom
Same behavior for both metal
and Se surfaces
One step type dominates
1µm
Almost no single dangling bond
steps observed!
Step-edge reconstruction
implied
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Layer NucleationNucleation at step edges implies a barrier to atoms crossing downward over steps or binding to the upper step edge.
Nuclei
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(220)/(204) Oriented CIGSLayers facet spontaneously into polar (112) type planes.
Smooth facets alternate with rough facets.
(220)/(204) epitaxial layer AFM image
Red: metal terminatedBlue: Se terminated
(112
) A
(112)BIndexing surface planes shows smooth planes are metal terminated
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(220)/(204) Oriented CIGS• Implication of the smooth/rough
surfaces:
(110) epitaxial layer AFM image
Diffusion transfers atoms to Se-terminated facets
Nucleation and growth on Se-
terminated surface.
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Composition Variations• EDS:• Probe size
~ 1nm
• Noisy data• No obvious grain boundary change• Data generally follows the tie line
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CIS/GaAs Epitaxy
Kirkendal Voidsw (112)Se facets
GaA
s
CuI
nSe 2
Angular Dark Field Image
Stacking faults & twins at interface
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Voids• From surface data
we know faceting is common.
• Voids between grains in polycrystals.
• Voids within grains at twin terminations and dislocations.
Nanovoids!
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Surface Chemistry
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CIGS Surface Chemistry• Use very smooth (112) surfaces to
study chemistry by angle-resolved photoelectron spectroscopy.
Angle θ controls probe depth
θ
Photon in
Photoelectron out
d d/cos(θ) θ
X-ray/UV light source
Photoelectron energyanalyzer
sample
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Angle-resolved Measurements• No chemical shift
between (112)metaland (112)Se.
00.10.20.30.40.50.60.70.80.9
1
442 444 446 448 450
Binding Energy (eV)
• No chemical shifts with photoelectron take-off angle
Oxidized surface is (In,Ga) oxide
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Angle-resolved Measurements• Results show Cu-deficient Ga-rich
surface
Modelling suggests 1-2 monolayers with altered Cu-poor composition
Cu In Ga Se O0 0 28 6 660 37 0 0 63
18 16 0 6 6024 16 10 50 024 16 10 50 0
Best fit by monolayer, at.%
Air-exposed
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The CdS Heterojuction• The best CIGS solar cells have a heterojunction
made by dip-coating CdS onto the CIGS.
• Plan: Use AR-PES to study the effect of the dip-coating bath on the surface.
CdS Dip HCl Etch
Control:HCl Etch w/o dip
CdS-coated sample
etched samples
CIGS
θ
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CdS Dip Coating Results• Results show ~0.7 cation monolayers of Cd atoms in
the first one (or two) atomic layers of the surface after etching.
• Fermi-edge shifts but core levels similar to sputtered & Se-capped samples.
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CdS Dip Coating Results• Comparison of
valence bands
• Metal-terminated has ~0.2 eV higher binding energy
• Dip & etch samples have component with ~1eV edge.
He I
The oxidized surfaces have a minority component (1%) consistent with the sputtered edge
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Conclusions• Copper chalcogenides are fascinating and unique
materials.
• Defects dominate the optoelectronic properties.
• Growth mechanisms are unique and interesting.
• Thanks again to everyone who helped with this research, funded it, discussed results with me, and to you for listening!