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STANFORD
JSH-1
GaInNAs:A new Material in the Race for
Long Wavelength VCSELsJ. S. Harris
S. Spruytte, C. Coldren, M. Larson,M. Wistey, V. Gambin, W. Ha
Stanford University
Agilent Seminar, Palo Alto, CA14 February 2001
STANFORD
JSH-2
Outline
l Introductionl The Choicesl GaInNAs/GaAs Material Propertiesl Work at Stanford
l MBE Growthl Edge-emitting lasersl Pulsed broad area VCSELsl CW oxide-confined VCSELs
l GaInNAs as an Enabling Technologyl Summary
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STANFORD
JSH-3
Exponential Growth inBandwidth Demand
STANFORD
JSH-4
Link Capacity Improvements
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STANFORD
JSH-5
Skiing Optical Fiber Networks
After Prof. Alan Willner-USC
Beginner Intermediate AdvancedBunny Extreme
OC-482.5 Gbs
OC-19210 Gbs
OC-76840 Gbs
OC-3072160 Gbs
OC-12622 Mbs
STANFORD
JSH-6
Fiber Distancevs. Bit Rate
0.01
0.1
1
10
100
1000
0.1 1 10 100 1000 104
Attenuation Limited
Dispersion Limited
Gigabit Ethernet
1550nm DFB-SMF
1310nm DFBOr VCSEL-SMF
1310nm FP-SMF
Bit Rate (Mb/s)
Tra
nsm
issi
on D
ista
nce
(km
)
850nm 50µm-MMF
VCSEL1310nm 50µm-MMF
850nm 62.5µm-MMF
10 Gigabit Ethernet
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STANFORD
JSH-7
Need for BandwidthTechnological Trends
l Computer performance continues to follow Moore’s Lawl Doubling of computing power every 18 monthsl Device research indicates exponential growth until 2010 (SIA roadmap)
l Network capacity is also increasing exponentiallyl Gilder’s Law – “Communication Capacity will triple every 12 months”l Growth at a rate greater than Moore’s law requires new technologies
l Required network capacityl Desktop bandwidth needs limited only by the human eye ~2 Gbpsl Internet traffic is non locall Number of users and hosts is growing exponentially
l Need long wavelength, high speed, low cost VCSEL
STANFORD
JSH-8
● Advantages of long wavelengths (>1300nm) relative to shortwavelengths (850nm):1. Fiber system performance
Installed multimode-fiber: optimized for 1300nmStandard singlemode fiber: >1260nm
2. Eye safety3. CMOS voltage scaling compatibility4. Si substrate transparency for integration
● Approach: Long wavelength active region on GaAs substrateLeverage 850nm VCSEL technology
High performance GaAs/AlAs DBRsAlAs-oxide current confinement and optical mode control
Long wavelength VCSELs
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STANFORD
JSH-9
Bandgap vs. Lattice Constantfor III-V Materials
InAs
AlSb
GaSbGeBULKSLE
(Ge)
α–SiC
GaSbInSb
AlSb CdTe
InAs
InN
GaN
AlN
ZnS MgSe
CdSAlP
CdSe
ZnTe
ZnSe
GaAs
GaPAlAs
InPSi
Lattice Constant (Å)
(.41 µm)
(.62 µm)
6.0
4.0
3.0
2.0
1.0
3.0 3.2 3.4 5.4 5.6 5.8 6.0 6.2 6.4
Ban
dgap
ene
rgy
(eV
)
(1.24 µm)
VisibleSpectrum
(.31 µm)
(.21 µm)
STANFORD
JSH-10
● GaNAs bandgap bowing Rapid decrease in bandgap.● N is small● In is large
Material Choices at 1.3µmLattice Matched to GaAs
control tensile/compressive strain on GaAs}
InxGa1-xAsyP1-y
InxGa1-xAs
InP
GaNyAs1-y
InNyAs1-y
980nm
GaxIn1-xNyAs1-y
on GaAs
AlAs
InAs
InxAl1-xAsAlxGa1-xAs
GaAs
0
0.5
1
1.5
2
2.5
5.4 5.5 5.6 5.7 5.8 5.9 6 6.1 6.2
Ban
dgap
(eV
)
1300nm1550nm
Lattice Parameter (Å)
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Page 6
STANFORD
JSH-11
GaInNAs/GaAs vs.InGaAsP/InP
2. Thermal conductivity●AlAs/GaAs higher thermal conductivity thanternary or quaternary lattice matched to InP●Heat removed through bottom DBR●High termal conductivity DBR required
increasing Ncontent
AlGaAs InGaNAs
1. Larger refractive index differences● n(AlGaAs)> n(InGaAsP)●Easier to make high reflectivity DBR mirrors
3. Larger conduction band offset●Better thermal performance for lasers
4. Better compositional control
N+ substrate
n1
n2
n1
R = r1 + r2 + r3 + …add in phase
n1- n2rn= n1+ n2
STANFORD
JSH-12
Overview MBE System
n Source of elemental Ga(0.1-0.8 monolayers/s)
n Source of elemental In(0.2-0.3 monolayers/s)
n As cracker supplies As2(beam flux = 20 _ totalbeam flux of III-elements)
n Radio frequency (rf)plasma supplies atomic N
n RHEED monitors growthn Substrate temperature
(phase segregation)
n Control nitrogen concentrationn Low concentration of impuritiesn Nitrogen bypassn Sharp QWs
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STANFORD
JSH-13
Characterization rf Plasma
n Ratio of intensity atomic nitrogen peak and intensitymolecular nitrogen peak relative amounts of atomic andmolecular nitrogen in plasma.
n Area under the peaks total amount of nitrogen in plasma.
6000 7000 8000 90000
0.05
0.1
0.15
0.2Atomic Nitrogen Transitions
Molecular NitrogenTransitions
STANFORD
JSH-14
Growth of GaN0.05As0.95thermodynamically stable atl low temperature.l high As2 flux.
300 400 500 600 700 800 900 100010
-25
10-20
10-15
10-10
10-5
5% GaN
no phase segregation
phase segregation
MBE Window
Growth Temperature andPhase Segregation
Film grown at 700 °Cl less N because 2NG N2
G.l second phase observed.
65 70 75 80 8510
0
102
104
106
Grown at 500 °C
Grown at 700 °C
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STANFORD
JSH-15
Control of NitrogenComposition by MBE
Nitrogen concentration inversely proportional to group IIIgrowth rate Unity N sticking coefficient!!
0 0.5 1 1.5 2 2.5 30
2
4
6
8
10
HRXRD SIMS HRXRD from superlatticeElectron Microprobe Anal
STANFORD
JSH-16
Sharpness of GaInNAsQuantum Wells
l QW boundary : 2-3 ML thickl QW thickness : 22 ML (=6.25 nm)l Dislocation free
GaAs
Ga0.8In0.2N0.015As0.985
65?
GaAs10 Å
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Page 9
STANFORD
JSH-17
PL measurements fordifferent N concentrations
l Luminescence efficiency of InGaNAs decreaseswith increasing N concentration
In0.3Ga0.7NAs QW
In0.3Ga0.7NAs QW
GaAs Barrier
GaAs Substrate
GaAs barrier
13
0?
65
?6
5?
In0.3
Ga0.7
As QW
GaAs Barrier
In0.3
Ga0.7
As QW
GaAs cap
13
0?
65
?6
5?
1 1.1 1.2 1.3 1.40
0.1
0.2
0.3
0.4
0.5InGaAs wells InGaNAs wells
0.6 % Nitrogen
1 at % Nitrogen
STANFORD
JSH-18
Effect of Anneal onPL properties of GaInNAs
1.15 1.2 1.25 1.3 1.35 1.40
0.5
1
1.5
2
2.5
3
3.5
4not annealedannealed
Annealing (RTA 1 min at 760 °C) of GaInNAs:l Improves luminescence efficiency by factor 50.l Shifts the peak to shorter wavelengths by 100 nm.
Anneal during growth of subsequent layers.
GaAs cap
GaAs cap
GaAs Barrier
GaAs substrate
Al0.33
Ga0.66
As cap
Ga0.7In0.3N0.02As0.98 QW
Ga0.7In0.3N0.02As0.98 QW
10
0?
15
0?
10
00
?7
0?
20
0?
70
?
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Page 10
STANFORD
JSH-19
Origin of low PL efficiency:C-V Measurements
l Not annealedGaNAs QWscontain defectsthat trapcarriers.
GaAs 3.1016/cm3 Be
GaAs 3.1016/cm3 Be
GaN0.03As0.97 3.1016/cm3 Be
GaAs p-substrate
200nm
50nm
1000nm
C-V measurements at300 K and 1 MHz
GaAs 3.1016/cm3 Si
GaAs 3.1016/cm3 Si
GaN0.03As0.97 3.1016/cm3 Si
GaAs n-substrate
500nm
50nm
1000nm
100 200 300 4000.0
0.2
0.4
0.6
0.8
1.0annealednot annealed
N C-V
(1017
cm
-3)
Depth (nm)
200 400 600 800 1000 12000.0
0.2
0.4
0.6
0.8
1.0
1.2 not annealedannealed
N C-V
(1017 c
m-3 )
Depth (nm)
l Annealing freescarriers(holes+electrons)in GaNAs QW.
STANFORD
JSH-20
Origin of PL shift:SIMS Measurements
Indium diffusing less than Nitrogen.ñShift of PL in GaInNAs caused predominantly by
nitrogen diffusion.
120 130 140 150 160 170 1800
100
200
300
400
500not annealedannealed
120 130 140 150 160 170 1800
5000
10000
15000not annealedannealed
Indium concentration profile Nitrogen concentration profile
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STANFORD
JSH-21
l Nitrogen is not all substitutional.l Amount of non-substitutional Nitrogen is
decreased by annealing.
Counts Aligned <100> Unaligned Ratio
Not annealed 102 390 0.262 ± 0.03
Annealed 59 369 0.160 ± 0.02
Origin of low PL efficiency:Interstitial Nitrogen
l Channeling combined with Nuclear ReactionAnalysis (NRA) to determine location of nitrogen.
l 14N + 3He 16O + proton.l 2.5 MeV 3He analysis beaml 1.5 MeV protons detected
min = 0.06for RBS channeling
STANFORD
JSH-22
In-plane Laser Results
l Broad area diodelaser
l 70 Å Single QW laserl Jth = 450 A/cm2
1.5 µmp-Al0.33Ga0.67As
1.5 µmn-Al0.33Ga0.67As
n+ GaAssubstrate
0.1 µmGaAs
0.1 µmGaAs
7 nmIn0.3Ga0.7N0.02As0.98
quantum well
0
10
20
30
40
50
60
0 1 0 0 2 0 0 3 0 0 4 0 0
Current (mA)
20µm X 840µm deviceJth = 450A/cm 2
=1.22µm
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STANFORD
JSH-23
Quantum Well Edge-Emitter Thermal Performance
Wav
elen
gth
(n
m)
Wavelength vs. Temperature
1235
1240
1245
1250
1255
1260
30 40 50 60 70 80 90Heatsink Temperature (˚C)
InGaNAs TQW Edge-EmitterL=800µm, lambda=1.24µm
0.4nm / º C
Th
resh
old
Cu
rren
t (m
A)
Threshold vs.Temperature
120
140
160
180
200
220
240
290 300 310 320 330 340 350 360
Heatsink Temperature (K)
InGaNAs TQW Edge-Emitter L=800µm, lambda=1.24µm
T0 ~ 140K
Ith = I0exp(T/T0)
Ü Good thermal performance: high T0
STANFORD
JSH-24
High Power GaInNAs EdgeEmitting Laser (Infineon/Ioffe)
D.A. Livshits, A. Yu. Ergov and H. Riechert, Electonics Letters 36, 1382 (2000)
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Page 13
STANFORD
JSH-25
Initial VCSEL Results
n+ GaAs substrate
22.5 pair n-GaAs/n-AlAs
DBR
20 pair p-GaAs/p-AlAs
DBR
Ti-Au
GaInNAs/GaAs triple quantum well
active region
substrate emission
50µm
0
4
8
12
16
20
0 100 200 300 400 500
Output power
Voltage
Ou
tpu
t P
ow
er (
mW
), V
olt
age
(V)
Current (mA)
1190 1195 1200 1205 1210
Inte
nsi
ty (
a.u
.)
Wavelength (nm)
l Jth = 2.5 kA/cm2
l Efficiency 0.066W/Al 1.2 m emissionl Pulsed operation
STANFORD
JSH-26
GaInNAs Oxide-ConfinedVCSEL
l Device Structure
Ti/Au reflector/top contact
17 pairs p-GaAs/AlAsprotected from oxidation
22 pair n-GaAs/AlAs DBR
3 GaInNAs/GaAs70Å/200Å active region
λ cavity
3 pairs p-GaAs/AlAsor GaAs/AlOx
SiO2 oxidation cap
bottom n-contact
Substrate emission
Mesas etch#1, SiO2 dep.
Mesas etch#2
Wet oxidation
l Process Highlights
Unoxidized aperture
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Page 14
STANFORD
JSH-27
Oxide-confined GaInNAsVCSEL pulsed characteristics
l 3.6 - 29 µm square aperturesl 0.9 - 20 mA threshold currentl Current density down to 2 kA/cm2
l Slope Efficiency up to 0.09 W/A
0.1
1
10
100
Thr
esho
ld C
urre
nt (
mA
)
Dimension (µm)
0
0.5
1
1.5
2
2.5
0
5
10
15
20
0 10 20 30 40 50
Out
put P
ower
(m
W)
Vol
tage
(V
)
Current (mA)
RT 200ns/100µsλ = 1.2µm
4.3µm
10µm
15µm
29µm
0
1000
2000
3000
4000
5000
6000
7000
0.05
0.06
0.07
0.08
0.09
0.1
0 5 10 15 20 25 30
Cur
rent
Den
sity
(A
/cm
2)
Slo
pe E
ff. (
W/A
)
Dimension (µm)
l Characteristics vs. sizel Typical L-I-V curves
STANFORD
JSH-28
Oxide-confined GaInNAs VCSELRoom Temp. CW Operation
Output Power vs Current
-90
-80
-70
-60
-50
-40
1195 1200 1205 1210 1215
Log
Inte
nsity
(dB
, arb
. ref
.)
Wavelength (nm)
1.3 mA
3 mA
3.5 mA
>40 dB
Spectra (5µm x 5µm)
l 5µm aperture: 1.3 mA threshold current; 3.6µm: < 1 mAl CW operation in spite of very high voltage drop (~9V) in top mirror
0
0.02
0.04
0.06
0.08
0.1
0
2
4
6
8
10
12
14
16
0 1 2 3 4 5
Out
put P
ower
(m
W)
Vol
tage
(V
)
Current (mA)
RT CW
5µm x 5µmIth = 1.32 mA0.0451 W/AVth = 10.3 V
3.6µm x 3.6µm
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Page 15
STANFORD
JSH-29
Oxide-Confined VCSEL:CW Thermal Analysis
l ~60°K temperature rise atpeak power
l Thermal ImpedanceZT 1/diameter
l ZT (5µm) = 1.24 K/mW(ZT, 50µm etched pillar = 0.36 K/mW)
l ZT(5µm) / ZT(50µm) = 3.6l Ith(5µm) / Ith(50µm) = 1/50l Reduce dissipated power in
pDBR for higher outputpower1200
1201
1202
1203
1204
1205
0 10 20 30 40 50
0
10
20
30
40
50
60
Wav
elen
gth
(nm
)
Dissipated Power (mW)
RT CW5µm x 5µm0.0924 nm/mW1.24 K/mW
Tem
pera
ture
Ris
e (°
C)
pulsed 0.2ns/10kHz
STANFORD
JSH-30
Challenge for Longwavelength GaInNAs
l Post annealing process is required to improvematerial quality after growth
l Nitrogen out-diffuses from quantum wellsl Emission spectrum blue-shifts due to nitrogen
loss
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Page 16
STANFORD
JSH-31
Advantages ofGaNAs Barrier
l Decreased carrier confinement Emission atlonger wavelengths.
l Decreased nitrogen out-diffusion during theanneal less shift of peak energy duringanneal (65 meV versus 74 meV).
l Strain compensation possible (GaAsN tensile /GaInNAs compressive).
E1
HH1
λ~1.36µm
GaInNAsQW
GaAs Matrix
E1
HH1
λ~1.44µm
GaInNAsQW
GaNAs Matrix
STANFORD
JSH-32
1.2 1.25 1.3 1.35 1.4 1.450
0.2
0.4
0.6
0.8
1GaNAs barriers annealed GaAs barriers not annealed xGaAs barriers annealed
GaAsN BarrierPL Measurements
Use of GaNAs barriers instead of GaAs barriers results in:l PL peak at 1.44 m instead of 1.36 m for not annealed sample.l PL peak at 1.34 m instead of 1.26 m for annealed sample.
GaAs cap
GaAs cap
GaN0.03As0.97 Barrier
GaAs substrate
Al0.33Ga0.66As cap
Ga0.65In0.35N0.02As0.98 QW
Ga0.65In0.35N0.02As0.98 QW
100?
150?
800?
65?
200?
65?
GaN0.03As0.97 Barrier200?
GaN0.03As0.97 Barrier200?
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Page 17
STANFORD
JSH-33
GaAs Barrier GaInNAsQuantum Well
l 4 Ga0.65In0.35N0.033As0.967 quantum wells and 2InGaAs quantum wells were grown
l GaAs Barriers between Quantum wellsl As grown sample : PL peak at 1.286 ml Annealed at 780oC(Highest PL intensity) : PL
peak at 1.222 ml PL blue-shift : 64nm
STANFORD
JSH-34
GaAs Barrier PL vs.Annealing Temperature
4GaInNAs & 2 InGaAs Quantum wells (GaAs barrier)
00.00050.001
0.00150.002
0.00250.003
0.00350.004
0.0045
8000 9000 10000 11000 12000 13000 14000
wavelength
PL in
tens
ity
(a.u
.) As grown720C 1 min740C 1min760C 1min780C 1min800C 1min820C 1min
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Page 18
STANFORD
JSH-35
GaNAs Barrier GaInNAsQuantum Well
l 4 Ga0.65In0.35N0.033As0.967 quantum wells and 2InGaAs quantum wells were grown
l GaNAs Barriers between Quantum wellsl As grown sample : PL peak at 1.336 ml Annealed at 780oC(Highest PL intensity) : PL
peak at 1.368 ml PL red-shift : 32nm
STANFORD
JSH-36
GaNAs Barrier PL vs.Annealing Temperature
n149
0
0.0002
0.0004
0.0006
0.0008
0.001
0.0012
0.0014
8000 9000 10000 11000 12000 13000 14000
Wavelength
PL in
tensi
ty (
a.u.) As grown
720C 2 min740C 1min760C 1min780C 1min800C 1min820C 1min
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Page 19
STANFORD
JSH-37
In-Plane Lasers with GaNAsBarriers
l Broad area in-plane laser.l 3 Ga0.65In0.35N0.02As0.98 QW’s inserted between GaAsN
barriers.l Lasing wavelength: 1.296 m.
0 100 200 300 4000
2
4
6
8
10
12Room TemperaturePulse Length: 200 ns, Period: 10 s20 m x 800 m
Ith
= 334mA, Jth
= 2.1 kA/cm2
Slope efficiency = 0.186 W/A
µ µ µ
1.29 1.295 1.3 1.3050
1
2
3
4
5
6
7x 10
-11
STANFORD
JSH-38
Characteristic Temperature
T0 = 105°K T0 = 146°K
GaAs Barriers GaNAs Barriers
280
290
300
310
320
330
340
350
360
5.2 5.3 5.4 5.5 5.6 5.7 5.8
y = -494.1 + 145.98x R= 0.94335
T (
Kel
vin)
ln(Ith)
280
290
300
310
320
330
340
350
360
5.6 5.7 5.8 5.9 6 6.1 6.2
y = -312.3 + 104.74x R= 0.83115
T (
Kel
vin)
ln(Ith)
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Page 20
STANFORD
JSH-39
GaInNAs: anEnabling Technology
l Many low cost photonic devices utilize vertical cavityconfiguration on GaAs substrates
l They don’t operate at communications wavelengths
l Significant technology base for GaAs based modulators,detectors, tunable lasers, free space optical interconnects
l Require long wavelength QW active regions that are latticematched to GaAs
STANFORD
JSH-40
Tunable VCSELs forSwitching and WDM
Space r Laye r
n-Dis t r ibu ted Bragg Re f lec to r
Quan tum We l l Ac t i ve Reg ion
& Cav i t y Space r
M e m b r a n e Contac t Pad
Defo rmab leM e m b r a n e Top Mi r ro r
Ai r Gap
p-con tac t
p -Con tac t Laye r
n -Con tac t Laye r Ant i -Ref lec t ive Coat ing
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Page 21
STANFORD
JSH-41
l Low insertion lossl Coupling controlled by active region lengthl Simple, low-cost bondingl Applicable to detectors, lasers and switches
GaAs Substrate
DBR mirror
Waveguide Core
Fiber BlockSide Polished
Fiber
In-Line Waveguide CoupledSemiconductor Active Devices
STANFORD
JSH-42
solder (1000 Å)n +
silicon
GaAsp AlGaAs
epoxy
i MQW
silicon
epoxy
silicon
anti-reflectioncoating
Quantum Well ModulatorsSolder-Bonded to Si ICs
K. W. Goossen et al.,IEEE Photonics Tech.Lett. 7, 360 - 362(1995)
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Page 22
STANFORD
JSH-43
Summary
l GaInNAs/GaAs is a promising material for long wavelengthVCSELs
l All epitaxial single-step growthl High T0 active layer with high-contrast thermally-conductive mirrorsl Easily controlled composition by MBE
l Demonstrated low threshold, RT, CW GaInNAs VCSELsl ~1 mA threshold current, 0.05 W/A slope efficiency at =1.2µml Peak output power limited by p-DBR resistance (~9V at Ith)l Demonstrated edge emitting lasers at 1.3µm and PL beyond 1.3µml GaInNAs is the best candidate for low cost, 1.3 µm VCSELs
l Future workl Rebuilding two chamber MBE system for high thruput, graded interface, C-
doped mirrors and VCSEL growthl Extend GaInNAs active QW material to tunable sources, modulators,
semiconductor optical amplifiers, optical IC interconnectsl Apply GaInNAs active devices to Si optical interconnects
STANFORD
JSH-44
GaInNAs is easier to grow by MBEthan by MO-CVD
Some would say this is(BAD NEWS)2
The GOOD NEWS
Conclusion 2!!!
The BAD NEWSGrading & multiple Al composition GaAs/AlAs
mirrors are difficult to grow by MBE