Results of micron-spaced geometries produced by wet chemical etching and subsequent OMCVD growth on various GaAs surfaces are presented. The polar lattice increases the complexity of the process. The slow-etch planes defined by anisotropic etching are not always the same as the growth facets produced during MOCVD deposition, especially for deposition on higher-order planes produced by the hex groove etching

Bailey, Sheila G.

Landis, Geoffrey A.

Wilt, David M.

English

NASA Technical Reports Server

Chemical Etching and Organometallic Chemical Vapor Deposition 
on Varied Geometries of GaAs 
Sheila G.  Bailey, Geoffrey A. Landis, and David M. Wilt 
NASA Lewis Research Center, 
Cleveland, OH 14195 
Summary 
Results of micron-spaced geometries produced by wet chemical etching and subsequent OM- 
CVD growth on various GaAs surfaces are presented. The polar lattice increases the complexity 
of the process. The slow-etch planes defined by anisotropic etching are not always the same as the 
growth facets produced during MOCVD deposition, especially for deposition on higher-order planes 
produced by the hex groove etching. 
Introduction 
The technology of anisotropic etching t o  produce a geometrically structured surface [ref. 11 
has become increasingly important in raising the efficiency of silicon solar cells [ref. 21. Benefits 
of surface structure produced by anisotropic etching include reduced reflectance, oblique passage of 
light through the cell, and light trapping. These lead t o  the possibilities of increased efficiencies and 
reduced radiation damage. To date, however, little work has been done on the use of anisotropic 
etching for 111-V solar cells. Implementation of these geometrical improvements in GaAs solar cells 
will require an understanding of etch characteristics and the growth process of metal-organic chem- 
ical vapor deposition (MOCVD) on multiple crystallographic planes with micron-scale periodicity. 
Wet chemical etching has been shown [ref. 31 to be capable of providing a simple, inexpensive 
method for fabricating structures with less than two micron spacings. In previous work [3,4] we 
have demonstrated MOCYD growth on V-grooved surfaces. 
Anisotropic etching in GaAs is more complicated than on silicon due t o  the polar nature of the 
lattice [ref. 51. The (111) plane is chemically different from the (111) plane, and both etching and 
deposition will behave differently on the different surfaces. 
Figure 1 shows a representative solar cell structure using a structured surface. The surface 
structure we chose here utilizes V-grooves, rather than the pyramidally etched surfaces typically 
used in silicon cells, because of the difference in etch characteristics of (111) Gallium and the (111) 
Arsenic faces. 
We refer to  a plane as (111)Ga because the atomic nature of the surface consists of gallium 
atoms bonded to  arsenic atoms slightly below the surface by three bonds; likewise, (111)As surface 
consists of surface As atoms bonded to  G a  a t o m  slightly below the surface. 
Figure 2 shows the orientation of (111)Ga and (111)As faces on a (100) wafer. Since the (111) 
plane is a Ga plane, [ I l l ]  planes with an even number of barred indices, such as (111) or ( l i i ) ,  
will be gallium planes, while planes with an odd number of barred indices, such as (111) or (I i i) ,  
are Arsenic planes. The (111)Ga planes are the least reactive (slowest etching) planes, and are the 
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planes preferentially revealed in the anisotropic etch. Note that V-grooves running perpendicular 
to  one another on the same side are not equivalent; if the V-groove running in the (011) direction 
shows a (111)Ga planes, one perpendicular to  it (:.e., in the (011) direction) would show a (111)As 
plane. In general (111)As grooves cannot be formed by anisotropic etching. The (111)Ga V-groove 
on the back side is perpendicular to  one on the front side. 
Anisotropic Etching 
The process of etching V-grooves consists of 
(1) masking the surface with photoresist stripes, aIligned in the (011) direction; 
(2) etching in an anisotropic etch. 
Figure 3 shows a Scanning Electron Microscope (SEM) photograph of a surface after the pho- 
toresist step. The photoresist used was AZ 4110. The photomask we used produces fine groove 
spacings, either 4 . 2 ~  photoresist stripes separated by 1 . 3 ~  openings (“5.5 micron pattern”), or sep- 
arated by 2 . 8 ~  openings (“7 micron pattern”). 
Several anisotropic etches for GaAs exist [ref. 5). In this work, the etch used was the Caros 
etch, consisting of 5:l : l  proportions of H2SO4, H 2 0 2 ,  and H2O respectively. Etch temperature 
was 24’ C. This etch does not attack photoresist, so that the photoresist was sufficient to serve 
as a mask. We also looked at etches with different proportions [ref. 61, such as “vertical” etch 
(1:8:1 H ~ S O ~ : H ~ O ~ : H Z O )  and “horizontal” etch (1:1:50), which produced faster and slower etch 
rates respectively. 
Figure 4 shows the etch process when the photomask is aligned in the “correct” direction, i . e . ,  
stripes running in the (011) direction. The Caros etch proceeds much faster in the (100) direction 
than in the (111) direction; the (111)Ga is a slow-etch face. The V-grooves are nearly flat-bottomed 
during the etch process; the width of the flat decreases as the etch proceeds. As the etch nears 
completion, the photoresist is slowly undercut. To make sharp-topped grooves, we terminate the 
etch just before the photoresist is undercut at the groove tops, typically about two minutes into 
the etch for the groove spacings (7p periodicity) used here. For flat-topped grooves the etch is 
terminated earlier. The photoresist is then removed with acetone and the surface given a solvent 
clean before growth. 
Quite different results are shown when the photoresist stripes are oriented in the opposite (011) 
direction, as shown in figure 5. In this case the V-groove walls would be (111)As planes, however, 
the (111)As face is not a slow-etch plane, and V-grooves are not formed. Instead a “hex” groove 
is formed. The photoresist is undercut much more rapidly than in the V-groove etch. In this case, 
however, the GaAs is cut through even more rapidly, and the photoresist peels from the surface 
when the GaAs cuts through, leaving a narrow wedge of GaAs attached to the photoresist as shown 
in figure 5C. 
The bottoms of the hex-groove is slightly rounded, rather than nearly flat as in the case of the 
V-groove etch, a result of the divergent etch front, rather than convergent. 
The upward facing walls are (111)As and the downward facing walls are (441) Ga faces. 
Z 5  1 
Note that in this orientation the striations on the etched surface are much more pronounced 
than in the case of V-groove formation. This is due to  the fact that the (111)As plane revealed here 
is more easily attacked than the (111)Ga plane revealed by the V-groove etching. 
Some researchers [ref. 71 have seen “dovetail” grooves, as in figure 6, for stripes oriented in this 
direction, where the downward-facing walls are the slow-etch (111)Ga faces. We have not observed 
this groove shape in etches done on GaAs. 
Identification of Crystal Planes 
When specific crystal planes are identified here, identification is based on comparing angles 
measured on SEM photographs of a cleaved surface with theoretical angles of the crystal planes. 
Causes for error in the measured angle include residual distortions in the SEM photograph, mis- 
alignment of the grooves, cleavage at a slight angle from the theoretical cleavage plane, observations 
taken with the sample not perpendicular to the beam, and inaccuracies in the angle measurement. 
In samples with a MO-CVD overgrowth, the epitaxial layer can be seen in the SEM photograph 
as a brightness difference between the p and n type material. This voltage contrast results from the 
Fermi level changing from p to n which changes the probability of secondary electron emission, and 
thus the apparent brightness. 
Epitaxial Growth on V-Grooves 
Table 1 shows the conditions used for the epitaxial deposition. The growth rate is a strong 
function of crystal orientation [ref. 8,9], which can result in preferential formation of certain crystal 
planes, or “faceting” . 
Table One: MOCVD Growth Conditions 
Reactor:  Horizontal geometry cold-wall reactor; RF Induction heated substrate 
Sample clean: Solvent degrease followed by DI H 2 0  rinse and N2 blow dry 
Source: TMGa and AsHz (10% in Hz) 
Dopant:  Diethyl Zinc 
Growth Temperature: 620°C 
Growth Pressure: 190 Torr 
G a  Mole Fraction: 1.5 . 
V/III Ratio: 20 
Growth Rate:  About O.lp/min. 
In general, a crystal plane which is slow to etch will also be a plane which is slow to grow, since 
an etch process can be viewed conceptually as the reverse of a deposition process. However, since 
the kinetics of epitaxial growth are not identical to those of etching, it is not always true that the 
growth facets will necessarily be the same as those revealed by etching. 
Figure 7 shows a typical epitaxial growth on a fully etched normal V-groove. The interface 
between the n-type buffer layer and the n substrate shows as a narrow white line; the p surface layer 
252 
as a lighter color. The  gas flow for this growth was parallel to  the grooves. The  growth is slightly 
thicker toward the groove bottom. 
In this growth we found the (100) surface a t  the groove tops t o  grow at a rate about equal 
t o  that  on the (111)Ga surface of the groove walls. In other work (using slightly different growth 
conditions, [ref. 41) we have found growth on the (100) surface t o  be up to 2.2 times faster than 
that  on the (111)Ga face. 
Figure 8 shows a slightly more complex growth, on partially etched V-groove (1-minute Caros 
etch) with flat tops to  the grooves. In this case, two crystal planes are revealed. The angle between 
planes on the groove walls is about 10 degrees. (Note also that the tops of the grooves are slightly 
tilted. The  epitaxial growth follows the true (100) face, and the wafer is cut 4 degrees off (100)). 
Angle measurements show that  neither of these planes is the true (111); the planes are tilted 
5 degrees off (111) respectively toward and away from (110). This is reasonable if the (100) faces 
on the tops and bottoms of the grooves grow slightly faster than the (111)Ga face on the sides of 
the grooves. The (divergent) faster growth a t  the (100) groove tops tends to  stabilize planes tilted 
slightly more than ( l l l ) ,  while the (convergent) faster growth a t  the (100) groove bottoms tends to 
stabilize planes tilted slightly less than (111). 
Expitaxial Growth on “Hex” Grooves 
Figure 9 shows MOCVD growth on the hex orientation groove. In this sample the grooves 
were etched about 30 seconds. The deposition forms facets of high-order planes. The original (100) 
surface has been faceted with (111)As faces. The bottoms of the grooves are beginning to  develop 
(411) facets. 
Figure 10 shows the results when growth is done on a hex-groove which has been etched to 
completion (ie., until the groove walls cut through and the photoresist spontaneously peels, as seen 
in figure 5C). In this case, quite clear (411) facets form on the bottoms of the grooves. 
The (411) plane is, like the ( l l l ) ,  a polar plane. As seen in figure 11, the (411) plane can be 
cleaved in such a way that the exposed surface atoms are predominantly Ga atoms bonded to the 
surface with two bonds, with some As a t o m  bonded to the surface with three bonds. 
Figure 12 shows the groove walls and the edges of the (411) planes in more detail. The groove 
walls, nominally (1l l )As faces, are seen t o  be ridged. The actual surface consists of (211) facets. 
Conclusions 
The  polar nature of the lattice makes etching and chemical vapor deposition on GaAs a con- 
siderably more complex process than on non-polar material such as silicon. The slow-etch planes 
defined by anisotropic etching are not always the same as the growth facets produced during MOCVD 
deposition, especially for deposition on higher-order planes produced by the hex groove etching. 
253 
References 
[ 1.1 C.R. Baraona and H.W. Brandhorst, Jr., Eleventh IEEE Photovoltaic Specialists Converence, 
4448  (1975). 
[ 2.1 M.A. Green. S.R. Wenham and A.W. Blakers, Nineteenth IEEE Photovoltaic Specialists Con- 
ference, 6-12 (1987). 
[ 3.1 R.P. Leon, S.G. Bailey, G.A. Mazeris and W.D. Williams, Appl. Phys. Lett, 49, 945-947 
(1986). 
[ 4.1 S.G. Bailey, R.P. Leon and A. Arrison, Nineteenth I E E E  Photovoltaic Specialists Conference, 
421-426 (1987). 
[ 5.1 S. Adachi and K. Oe, J .  Electrochem. SOC., 130, 2427-2435 (1983). 
[ 6.1 S. Lida and K. Ito, J .  Electrochemical SOC., 118:5, 768-771 (1971). 
[ 7.1 P.M. Holm and R.J. Roedel, 17th IEEE Photovoltaic Specialists Conference, 921-926 (1984). 
[ 8.1 T. Nakanisi, J .  Crystal Growth 68,  282-194 (1984). 
[ 19.1 R.P. Gale, R.W. McClelland, J.C. Fan and C.O. Bozler, Inst.  Phys.  Conf Ser.  N o .  65, 
101-108 (1982). 
254 
Figure One: Sche.matic of V-gmve Gallium Arsenide Solar Cell (not to scale). 
(111) planes on (100) GaAs wafer 
Figure Two: (111) planes on (100) GaAs Wafer. There are two non+quivalent types of (111) 
plane; the (11l)Ga and the (111)A.s planes. Anisotropic etching preferentially defines the (111)Ga 
face. 
255 
Figure Three: SEM Photograph of Photoresist Stripes on GaAs Wafer. 
ORIGINAL PAGE 
BLACK AND WHtTE PHOTOGRAPH 
4A: after 15 seconds of etch 4B: after 30 seconds 
4C: after two minutes 4D: after removal of photoresist 
Figure Four: SEM Photographs of V-Groove Etch Process: 
257 
5A: after 20 seconds of etch 5B: after one minute d c t c h  
c: after one minute, showing etch-through and resist stripping 
Figure Five: SEM Photographs of “Hex” Groove Etch Process: 
ORfGINAL PAGE 
258 U C X  AND WHtTE PHOTOGRAPH 
ORIGINAL PAGE 
BLACK AND WHITE PHOTOGRAPH 
Figure Six: Some Experimenters have seen U ~ O v e ~ a i i n  cross-section gooves as shown above. None 
of our cyper iments produced this pattern. 
Figure Seven: SEJf Photograph of Cleaved Cross-section of Epitaxial p-n junction on f i l ly  v- 
Grooved Etched GaXs surface. 
Figure Eight: SEM Photograph of Epitaxial Growth on Partially V-Groove Etched Surface. 
SA: Before growth. SB: After growth. 
Figure Nine: Epitaxial Growth on “Hex” Groove: 
260 
ORiGlNAL PAGE 
BLACK AND WHlTE PHOTOGRAPH 
ORIGINP$L PAGE 
BUCK AND WHITE PHOTOGRAPH 
angle 19: (measured) 
angle 19 (theoxy) 
t 
Figure Ten: 
major planes. 
Epitaxial Growth on "Hex" Groove etched to Completion, showing orientation of 
26 1 
(411) Plane viewed in [110] direction 
Figure Eleven: G A S  Lattice, showing (411) Plane. Ga a t o m  (white) are held to the surface with 
two bonds, while As atoms (black) are held to the surface with three bonds. For the (411) surface, 
the situation is reversed. 
262 
(1 1 1) As with (21 1) facets 
nearly (100) 
Figure Twelve: Detail of EpitaGal Growth on UHexn Groove Etched to Completion, showing (211) 
facets on the (111)As face. 
263 


Chemical etching and organometallic chemical vapor deposition on varied geometries of GaAs

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