Reference

NBS

Publications

IMBSIR 81-2403

3

Gallium Arsenide Materials

Characterization: Annual Report,

October 12, 1978 to

October 1 2, 1 979

U.S. DEPARTMENT OF COMMERCE

National Bureau of Standards

National Engineering Laboratory ^

Center for Electronics and Electrical Engineering

Semiconductor Materials and Processes Division

Washington, DC 20234

December 1 981

li)0

lIKh

Electronics Technology and Devices Laboratory

nmouth, NJ 07703

19Z2

NATIONAL BtniEAa Of ITAKOANOa

UBRABT

NBSIR 81-2403

GALLIUM ARSENIDE MATERIALS ^

CHARACTERIZATION: ANNUAL REPORT,

^

OCTOBER 12, 1978 TO

OCTOBER 12, 1979

NOV 10

X X

i\- mu

I

J. R. Ehrstein and A. C. Seabaugh

U.S. DEPARTMENT OF COMMERCE

National Bureau of Standards

National Engineering Laboratory

Center for Electronics and Electrical Engineering

Semiconductor Materials and Processes Division

Washington, DC 20234

December 1981

Prepared for The U.S. Army Electronics Technology and Devices Laboratory

Fort Monmouth, NJ 07703

1982

-

's ^

X

U.S. DEPARTMENT OF COMMERCE, Malcolm Baldrige, Secretary

NATIONAL BUREAU OF STANDARDS, Ernest Ambler, Director
V . • . .i I ;

.‘HD ’ 'i'C‘
CONTENTS

Page

Abstract 1

1 . Introduction 1

2. Electrical Contacts to Gallium Arsenide 1

2.1 Introduction ......... . . 1 2.2 Contacting and Profiling Experiments . 3 2.3 Discussion ....... .............. 10

3. Spreading Resistance Measurements 11

3.1 Introduction ..... 11 3.2 Background 11 3.3. Limitations Imposed by Commercial Instrumentation 12

3.4 Measurement Variables Tested 15

3.5 Experimental Results With Bulk GaAs 15

a) Effect of Probe Material and Probe Load 15

b) Effects of Specimen Surface Preparation 18

3.6 Experimental Results With Implanted Layers in GaAs 22

a) Beryllium (p-Type) Layer Profile Data 22

b) Calibration of Implanted Layer Profile 22

c) Anomalous Differences in Sensitivity to Probe Force .... 26

d) Silicon and Selenium (n-Type) ’ Layer Profile Data 26

3.7 Summary °. . 28

3.8 Recommendation 32

References 33

LIST OF FIGURES

Page

1. Schematic summary of the potential profiling technique 6

2. Schematic diagram of potential profiling circuit 7

3. Potential profiles of a 2 fl»cm rz-type silicon specimen 8

4. Potential profile of a 10^ f^»cm chromium-doped GaAs specimen ... 9

Graph of the measured resistance as a function of time during a single measurement cycle for probes on GaAs showing poor settling

characteristics 13

iii

5
LIST OF FIGURES (continued)

Page

6. Actual measured resistance for five measurement cycles using a tungsten-osmium probe on 135 fl»cm n-type silicon polished with

0.5-Mm diamond 14

7. Dynamic probe response for six measurement cycles on silicon-doped

bulk GaAs as polished by the manufacturer 19

8. Photomicrographs of typical good surfaces obtained on different

bulk GaAs specimens with four preparation procedures 20

9. Photomicrograph showing gross surface break-up or crumbling which

was sometimes encountered during beveling of GaAs specimens ... 21

10. Surface finish and spreading resistance data for silicon-doped

bulk GaAs specimen which had been top-surface polished with 1-ym

diamond bonded by plastic tape and then beveled with O.S-ym diamond against ground glass 23

11. Specimen surface finish and profile data for beryllium-implanted

GaAs which has been beveled by two different procedures 24

12. Four sets of spre°ading resistance depth profile measurement on beryllium-implanted GaAs showing repeatability generally obtained

on a specimen beveled with 0.5-ym diamond 25

13. Dopant density depth profile for a beryllium-implanted GaAs specimen beveled with 0.5-ym diamond against ground glass 27

14. Dopant density profile predicted according to the procedure of

Winterbon for the selenium-implanted layer shown in figure 16a . . 29

15. Dopant density profile predicted according to the procedure of

Winterbon for the silicon-implanted layer shown in figure 1 6b . . 30

16. Two-probe resistance profile data for selenium layer implanted

into GaAs at 300 keV with a fluence of 5 x 10^*^ cm“^ , and

silicon layer implanted into GaAs at 170 keV with a fluence of

5 X 10^2 ^j„-2 3T

LIST OF TABLES

Page

1. List of GaAs Specimens Available for Tests 16

2. Probes Available for Test 17

3. Surface Preparation Media Used 17

IV
Gallium Arsenide Materials Characterization

by

J. R. Ehrstein and A. C« Seabaugh

Semiconductor Materials and Processes Division

National Bureau of Standards

Washington, DC 20234

ABSTRACT

Ohmic and Schottky barrier contacts for use in electrical characterization were examined both conceptually and experimentally with

particular focus on the problems associated with ohmic contacts to

semi -insulating GaAs, The conductivity type of the semi -insulating

material, which can be either n- or p-type, was investigated by

means of a potential profiling technigue. In addition, the feasibility of spreading resistance measurements was examined and applied to both low resistivity bulk GaAs and ion-implanted semiinsulating substrate material.

Key words; contacts; gallium arsenide; potential profiling;

spreading resistance.

1. INTRODUCTION

The superior electronic properties of gallium arsenide (GaAs) for the fabrication of high-speed digital, microwave, and optoelectronic devices and circuits are required in a number of government and industrial applications.

However, there are many unsolved problems in materials growth, material characterization, device fabrication, and device characterization which must be

surmounted before the full potential of GaAs can be realized. This report is

concerned with the material characterization aspects of these problems, in

particular the nature of metal semiconductor contacts for transport measurements and spreading resistance measurements.

2. ELECTRICAL CONTACTS TO GALLIUM ARSENIDE

2.1 Introduction

A nontrivial part of any electrical characterization program is the development of reliable and reproducible contacting techniques. Care must be taken

to ensure that the formation of contacts does not alter the properties of the

material or adversely influence the desired characterization technigue. It

is well known that arsenic dissociates from a GaAs surface during heat treatments at temperatures as low as 300°C. Since the effective sintering temperature of most contact metals is greater than 300°C, there are unique problems

in contacting GaAs. Processing temperatures must be kept as low as possible,

and the specimen must be kept at these temperatures for as short a time as possible in order to minimize this problem.

1
In general, metals and alloys for making ohmic* contacts to semiconductors

are chosen on the basis of two guidelines [ 1 ] ; ( 1 ) a material of high work

function is chosen for p-type material and low work function for rs-type material and (2) the metal should form a region of high majority carrier density

under the contact after an appropriate alloy cycle. If these guidelines are followed, the width and height of the metal-semiconductor potential barrier

is reduced, thus increasing the probability of conduction by both thermionic

emission over the barrier and tunneling through the barrier. Conversely,

metals for Schottky barriers'*’ are chosen for (1) their low work function

for p-type material and high work function for n-type material and (2) their

inability to form a high carrier density region under the contact. These

guidelines lead to large barrier width and height, thereby decreasing the

probability of thermionic emission over the barrier or tunneling through the

barrier. For GaAs, the barrier height is only weakly dependent on the metal

work function due to the high surface state density which pins the Fermi

level at the metal-semiconductor interface. Therefore, the properties of

Schottky-barrier contacts to GaAs are only a weak function of the metal

used.

Semiconductors can be divided into three categories which distinguish between

the dominant effects determining the Fermi level position at the contact

interface [2].

1 . The Fermi level at the interface is a function of metal work function, semiconductor electron affinity, and semiconductor doping

(e.g. , cadmium sulfide).

2. The Fermi level is pinned at the surface due to ‘intrinsic surface

states (e.g., germanium, silicon).

* In this work, an ohmic contact is defined as a metal-semiconductor contact

exhibiting negligible voltage drop with respect to the device voltage. For

example, in the case of two similar contacts formed on a bulk semiconductor, a linear current-voltage characteristic, with current passing through

the contacts and the voltage measured across the contacts (over a voltaae

range typical for the device), is termed ohmic,

t In this work, a Schottky barrier contact is defined as a metal-semiconductor contact (i.e., not a p-n junction contact) whose current-voltage characteristic can be approximated by the relation

is the current in A, Ig is the reverse bias saturation current in

the electron charge equal to 1.602 x 10~^^ C, V is the voltage across the contact in V, k is the Boltzmann constant equal to 1.38

J/K, and T is the absolute temperature in K. A Schottky barrier

can often be distinguished from a p-n junction contact by the

of minority carrier injection under forward bias conditions.

where I A, q is

applied

X 10“23

contact

absence

2
3. The Fermi level is pinned at the surface due to extrinsic surface

states (e.g. , gallium arsenide, indium phosphide, aluminum antimonide)

.

For a category 1 semiconductor, the barrier height, gcfjg, for electrons and

holes, respectively, is described by [3],

qc}) = q ( (|) ~ x) n=type semiconductors

B m

n

= E - q ( d) “ x) P“type semiconductors

B g m

^ j IT P

where q(()jf, is the metal work function in eV, qx is the semiconductor electron affinity in eV, and Eg is the energy band gap in eV. Schottky barrier

image force lowering has been neglected in these expressions, but could easi

ly be included without qualitatively altering the discussion. In principle,

a metal work function can be chosen such that ' 'thus

q<j) m

E—g

+ qx .

For this choice of metal work function, a barrier contact will be formed to

the semiconductor independent of the conductivity type. This is desirable in

potential profiling measurements to determine the conductivity type of category 1 semiconductors.

When the Fermi level is pinned at the metal-semiconductor interface by surface states as in categories 2 and 3, the Schottky barrier height is given by

the difference between the majority carrier band edge and the energy level at

which the Fermi level is pinned, Epp, in eV. For n-type material, this is

n FP /

where E^ is the conduction band edge in eV. For p-type material

q<l>, = E.FP

E

V ,

where E^ is the valence band edge.

Using this simple model, then, and the fact that the Fermi level at the GaAs

surface has been found to be pinned at roughly midgap [4,5,6], a metalsemiconductor contact to n- or p-type GaAs will typically form a Schottky

barrier contact. To form an ohmic contact, a region of high majority carrier

density must be formed under the contact. This highly doped region increases

the probability of carrier transport by tunneling through the barrier. If

this results in a negligible barrier voltage drop with respect to the device

voltage drop, the contact is termed ohmic.

2.2 Contacting and Profiling Experiments

There are a wide variety of techniques available for forming ohmic contacts

to GaAs. Among the most simple techniques are alloy regrowth and ultrasonic

soldering. In this work ohmic contacts were formed by both of these

techniques.

3
For the alloy regrowth method on n-type specimens (N^ - >10^^ cm“^ )

,

alloying was performed on a tantalum microstrip heater purged in an electronic grade forming gas atmosphere (95 parts nitrogen, 5 parts hydrogen by volume). Typically, the GaAs specimen was prepared by rinsing successively in

trichlorethylene, acetone, and methanol followed by a 1-min etch in a room temperature sulfuric acid-peroxide solution (3 parts sulfuric acid, 1 part

hydrogen peroxide, 1 part deionized water by volume). The specimen was then

rinsed in deionized water and blown dry with nitrogen prior to placement on a high purity graphite boat which provided physical isolation from the tantalum

heating element. Indium, tin, or indium-tin alloy spheres of 20-mil (0.51-

mm) diameter were etched in hydrochloric acid and placed directly onto the

GaAs surface through holes in a graphite mask used to align the spheres and

to prevent their rolling off. The system was subseguently purged for 10 min

at a flow rate of roughly one liter per minute before alloying. Temperature

was monitored by means of a type K thermocouple which was spot welded to the

bottom of the tantalum strip, and the process was continuously observed

through a microscope. In a typical process sequence the temperature was increased until the spheres melted and collapsed, the specimen was alloyed

for 30 s at the collapse temperature, the power in the tantalum heating element was then turned off, and the system was allowed to cool to room temperature. The contacts formed by this technique were found to be ohmic and suitable for electrical transport measurements.

Alloy regrowth ohmic contacts were also formed to n-type specimens after an electroplating technique described by Mattauch [7]. In this ohmic contact

process, a three-layer structure is utilized: tin-nickel, nickel, and gold.

The tin-nickel alloy is pulse-electroplated at approximately 1 A and 1 Hz

(with a 50-percent duty cycle). This layer is followed by a 1-min 20-mA dc

nickel electroplate and finally a 1-min 20-mA dc gold electroplate. The

tin-nickel/nickel/gold structure is then microalloyed in forming gas at approximately 200°C for 30 s. The contacts fabricated by this process were

also ohmic and used for single-probe response studies in the spreading resistance experiments of section 3.5.

Ohmic contacts are often desired on semi-insulating GaAs. In practice, this

is more difficult to achieve than for lower resistivity material. It is

desirable to know the conductivity type of the GaAs in order to make a suitable choice of contact metal (i.e., so as not to form a p-n junction). Conventional thermal-probe conductivity type determination on semi-insulating

material is often ambiguous due to the very low carrier density and resultant

small Seebeck voltage. Wolfstirn and Focht [8] have reported on a thermoelectric n-p tester for use on GaAs and gallium phosphide (GaP) using an ac bias to set up an imbalance between back-to-back hot and cold Schottky barriers .

A method recently described by Neumark et at. [9] for conductivi ty-type determination with application to high-resistivity material is potential profiling. According to this method, the conductivity type of a semiconductor

can be determined by the potential profile between two barrier contacts

across which a voltage is applied. By potential profiling, the preferred

direction of electron transfer across the barrier is known with respect to

the applied bias. This preferred electron transfer direction depends on the

majority-carrier conductivity type, assuming that the dominant transport

4
mechanism is by thermionic emission over the barrier. It is asserted that by

knowing the direction of preferred electron transfer and the polarity of the

applied bias, the conductivity type can be determined. This method is illustrated in figure 1 for both n- and p-type semiconductors. An energy band

diagram for the case of two symmetric barrier contacts to n- and p-type semiconductors under thermal equilibrium conditions is shown in figure la. The

energy band diagrams change as depicted in figure 1b when the same voltage is

applied across these barrier contacts with the polarity shown. Note that for

the same polarity of applied voltage, V^, the left-side barrier contact on

the n-type material is forward biased, while the left-side barrier contact on the p-type material is reverse biased. Similarly, the right-side barrier

contact on the n-type material is reverse biased, while the right-side barrier contact on the p-type material is forward biased. By profiling the

potential between the two-barrier contacts, these conditions can be detected

and the conductivity type determined. Figure 1c displays the expected potential profile (with voltage measured with respect to the left-side barrier

contact) for both the n- and p-type cases. The voltage drop due to the

specimen bulk resistance is represented by

Potential profiling can be implemented by using an array of barrier contacts

formed on the high resistivity material. A schematic diagram of this measurement is shown in figure 2. A voltage, , is applied to the Schottky

barriers at opposite ends of the specimen (contacts labeled 1 and n) and the

resulting voltage distribution is measured as the voltage, V, at the intermediate contacts, after adjusting V2 for zero current through the ammeter, A.

In this manner, no current is drawn from the specimen in the voltage measurement circuit, and an accurate deteriti'i nation of the potential of each of the

contacts can be made.

The apparatus (as shown in fig. 2) was assembled and the technique verified

on a 2 f2»cm n-type silicon specimen. The measured results are shown in figure 3 which is a plot of contact-to-contact voltage versus probed contact

position along a line of evaporated aluminum Schottky barrier contacts. As

depicted in figure 2, three probes were used to contact the specimen, each

consisting of a tungsten wire held in a micropositioner. Two probes used to

bias the specimen were placed on the end contacts and remained fixed, while

the third and central probe was used to probe the potential from left to

right. For the initial profile, with polarity as indicated in figure 2, the

potential was measured between the left-side end contact (i.e., contact #1 in

fig. 2. ) and the central probed contact. The current was then reversed and

the potential reprofiled with voltage measured with respect to the right-side

end contact. In figure 3, the initial profile of the specimen corresponds to

that expected for n-type material and shown previously in figure 1c. When

the current is reversed, the end contacts reverse roles: the leftmost contact becomes reverse biased, while the rightmost contact becomes forward

biased as indicated in the potential profile of figure 3. By comparing the

initial profile of figure 3 with the potential profiles expected (fig. 1c),

it is verified that the silicon specimen is n-type.

Results of applying this technique with evaporated gold Schottky barrier

contacts on semi -insulating GaAs are shown in figure 4. For the initial

profile with polarity as indicated in figure 2 and central probe stepped from

left to right, the potential difference between contacts 1 and 2 is greater

5
n - type P

" type

a. Thermal equilibrium

b. With applied bias

c. Potential profile

Figure 1. Schematic summary of the potential profiling technique. (a) Energy band diagram plotted against position for two metal-semiconductor barrier

contacts on n- and p-type semiconductors in thermal equilibrium. (b) The same systems with applied bias (V^) as specified. Vj^ is defined as the

voltage drop in the bulk region of the semiconductor. (c) Potential profile,

V, also plotted against position.

6
Figure 2. Schematic diagram of potential profiling circuit.

7
V

(VOLTS)

PROBED CONTACT

Figure 3. Potential profiles of a 2 n-type silicon specimen

barrier contact spacing is approximately 15 mil (0.381 mm).

Schottky
AFTER CURRENT REVERSAL

00

K“

O

3 4 5

PROBED CONTACT

Figure 4. Potential profile of a 10^ !^»cm chromium-doped GaAs specimen

Schottky barrier contact spacing is approximately 30 mil (0.762 mm).

9
than that between contacts 6 and 7 at the other end. When current through

the specimen is reversed (and the zero of potential taken at the opposite

end, i.e., contact 7), the converse of this situation occurs, with the potential difference between contacts 6 and 7 becoming greater than that between

contacts 1 and 2. Note that due to the high specimen resistance the asymmetry is not as pronounced as in the 2 fl»cm silicon specimen (fig. 3). The

result is opposite to that seen in the silicon specimen and for the given

polarity of applied bias corresponds to the profile expected for p-type material (see fig. 1c). This p-type conductivity indication was typical of both

the undoped and chromium-doped GaAs substrates profiled in this study.

With a knowledge of the semi -insulating GaAs conductivity type, it is possible to select an ohmic contact metal such that a p-n junction is not formed.

In this work, alloy ohmic contacts were attempted on semi-insulating GaAs

(using the technique previously described) without success, using high purity

indium, zinc, and indium: tin (50 parts In; 50 parts Sn by weight). Linear

current-voltage characteristics were achieved only when the surface converted

to low resistivity. Ohmic contacts to semi -insulating GaAs were successfully

formed in this work by ultrasonically soldering either indium-tin or indium

zinc alloys (50 parts In: 50 parts Sn or Zn by weight) at less than 150°C.

The specimen was then allowed to alloy on a hot plate in air at 150°C for 5 min. This method, however, was not reproducible for unknown reasons.

Schottky barrier contacts to both low and high resistivity GaAs can be

achieved routinely using conventional semiconductor processing techniques.

Gold Schottky barrier contacts were formed in this work by dc electroplating

and by vacuum evaporation.’ Electroplated contact definition was facilitated

by photolithographically defining ah array of holes in a pyrolytically deposited silicon dioxide layer. The gold was plated at 20 mA for 2 min with

no subsequent alloy step. Evaporation-deposited Schottky barriers were delineated during deposition by means of a 5-mil (0.13-mm) stainless steel

shadow mask.

2.3 Discussion

The problems encountered in making Schottky barrier and ohmic contacts (particularly to semi -insulating GaAs) were examined conceptually and in a few

preliminary experiments. Potential profiling as a means of conductivi ty-type

determination was examined and applied to high-resistivity GaAs. In summary,

the material properties that affect contact characteristics in GaAs include

Fermi level pinning at the surface due to surface states, the surface region

doping, and the metal work function (although very weak for GaAs). For the

specific problem of forming ohmic contacts, the surface region must be heavily doped to form a tunnelable barrier (e.g. , by alloying). However, since

this process must be done at low processing temperatures (in order to minimize arsenic out-diffusion), the choice of metals is restricted. This re- striction may well be overcome by capping the exposed GaAs surface (e.g.,

with silicon nitride), laser annealing the metal contact, or some combination

of these techniques. Ion implantation may offer the greatest flexibility and

control of ohmic contact formation since the surface region over which a contact is to be formed can be heavily doped prior to contact formation.

Future study should examine these technologies as well as investigate other

ohmic contact alloys such as gold: germanium.

10
3* SPREADING RESISTANCE MEASUREMENTS

3.1 Introduction

The objective of this subtask is to explore the applicability of the spreading resistance technique to the profiling of ion-implanted layers in GaAs.

Although a significant number of papers have been published concerning the

methodology and interpretation of spreading resistance measurements in silicon, only three publications address the use of point pressure contact

"spreading" resistance measurements in GaAs [12-14]. These papers report

measurements on diffused layers and epitaxial structures with multimicrometer

layer thickness. However, prior to the present report, no work has been

reported on submicrometer thick layers implanted into GaAs.

3.2 Background

The principal difficulty with applying the spreading resistance technique to

GaAs is that point pressure contacts using durable alloy probes (tungsten

alloys are used to make the measurement on silicon) are neither ohmic nor of

reasonably low resistance. In order to use point pressure contacts for re- sistivity profiling in GaAs, the problem of choosing specimen surface preparation and probe materials to obtain reproducible and acceptable contact

properties must be solved. Each of the reported works [12-14] uses a different approach to solving this problem, but none of them was applied to implanted or submicrometer layers.

One of the reported techniques [12] requires special metallization to the

probes (which offers reduced contact resistance, but has low durability) and

a special contact-forming circuit, while another [13] requires a silver paste

metallization stripe for a reference electrode, a large area silver paste

backside contact, and a 1-V measurement voltage for profiling. The third

technique, reported by Queirolo [14], appears to be the most flexible in that

instrumentation and techniques are used which are common for depth profiling

of silicon using the spreading resistance mechanism.

Since Queirolo 's approach was chosen as the basis for the work reported here,

it will be described in detail. Epitaxial and dif fused-layer specimens to be

profiled were beveled in a thick paste of 0.3-ym alumina in water, using a commercially available polishing fixture intended for preparing specimens for

spreading resistance measurements [15]. Following this surface preparation,

measurements made with tungsten-osmium probes, each loaded with 45 g, gave

acceptably stable measurements with absolute values low enough (<10® f2) to be

measured with commercial spreading resistance electronics [15]. However,

Queirolo reports that the measured resistances are much too large to be

characteristic of a spreading resistance; rather the measurement response

is dominated by metal-GaAs contact resistance. Ostensibly, the dopant

density in the GaAs under the contact controls the barrier resistance, at

least in the reported dopant concentration range, 10^^ to about 5 x 10^^

cm~^, and the measured two-probe resistance is approximately inversely proportional to the specimen's dopant density under the contacts. Under these

conditions, the geometric spreading resistance is a minor component of the

measured resistance, so the sampling volume correction factors normally used

to interpret spreading resistance profiles on a graded layer [16,17] are not

11
needed for measurements of GaAs profiles. As is noted by Queirolo, simple

calibration of contact resistance on specimens of known dopant density, which

have been prepared in the same manner as the test specimen, is sufficient for

profile interpretation.

Although he uses 0.3-ym alumina polishing as a best compromise for both pand n-type GaAs layers, Queirolo states that bulk p-type GaAs specimens of a given resistivity exhibit better reproducibility and lower contact resistance

when measurements are made on surfaces lapped with 5-pm alumina than when

made on surfaces polished with 0.3-um alumina. In contrast to this, he shows

that for bulk n-type specimens, lower contact resistance and apparently better reproducibility are obtained for measurements made on the polished surfaces. Thus the effect of specimen surface preparation on the resistance

measurements, which is perhaps due to specimen damage or to surface state

formation, is also apparently a function of specimen conductivity type. (An

interactive dependence of measurement quality on specimen preparation and

conductivity type - although different in specific details from that shown by

Queirolo - was also found in the present work in submicrometer implanted

layers and is discussed in secs. 3.5 and 3.6.)

3.3 Limitations Imposed by Commercial Instrumentation

It is desirable to use commercially available spreading resistance equipment

for two-probe resistance profiling of GaAs. It is useful, therefore, to

consider the normal mode of operation of such a system. The system at NBS is

automated and completes a spreading resistance measurement at a position on

the semiconductor in a fixed time interval, 6 s in the case of the present

measurements. The measurement cycle consists of .translating the specimen a preselected increment while the two probes are raised, lowering the probes to

the specimen surface with a 1 0-mV dc bias between the probes at the time of

contact, allowing about 1.25 s for the probe contact to settle (or stabilize)

to a constant resistance value, electrically sampling the probe-to-specimen

contact resistance during a "measurement window," and finally, lifting the

probes. The specimen is then translated and the measurement cycle is re- peated until the spreading resistance profile of the desired region of the

semiconductor is obtained. Figure 5 shows, on an expanded scale, the change

of resistance with time and the sequence of probe and stage motions for the

case of a pair of probes which do not settle to a constant contact resistance. (This lack of settling of contact resistance is sometimes found with

silicon and was very common in the present work on GaAs. ) In contrast, figure 6 shows a recorder tracing of the dynamic response, i.e., the log of

contact resistance versus time, for several measurement cycles with probes

having good probe-to-semiconductor resistance-settling characteristics. This

tracing was obtained on a 135 f^*cm n-type silicon specimen with a set of

tungsten-osmium probes used in the present GaAs study. The ability of the

probes to stabilize rapidly is an important requirement for obtaining

repeatable data. It is partly controlled by the cleanliness and general

condition of the probes, but in the case of GaAs, it was found to be more strongly controlled by the condition of the specimen surface, as will be

shown below. A second requirement for obtaining acceptable data, particularly important in the case of GaAs, is that the contact resistance stay below

about 10^ fl. Although the commercial spreading resistance electronics can obtain accurate measurements of contact resistance up to about 10^ the

12
MEASURED

RESISTANCE

I

ii

I

Figure 5. Graph of the measured resistance as a function of time during

a single measurement cycle for probes on GaAs showing poor settling charac

teristics.

13

Probes

descend
TIME Is)

Figure 6. Actual measured resistance for five measurement cycles using a tungsten-osmium probe on 135 fi»cm n-type silicon polished with 0. 5-ym diamond. This sample shows good probe-settling characteristics.

14
time required for the electronics to stabilize increases for resistance values above about 10^ U, and this time may be longer than allowed by the automatic timing cycle. The time requirement for stabilization becomes even more difficult to satisfy if capacitive charging effects are encountered at the

probe-semiconductor interface. The practical implication is that resistance

readings much above 10® on GaAs are suspect since the electronics have

probably not stabilized prior to the measurement sampling window (fig. 5).

3.4 Measurement Variables Tested

The experimental factors which control the reproducibility and the general

quality of two-probe resistance (spreading resistance) measurements were studied on both bulk and ion-implanted GaAs specimens. Several specimen

preparation methods were tested to evaluate their relative effect on contact

stability, measurement repeatability, and absolute value of contact resistance. A number of probe materials and a few modifications to the common

tungsten-osmium alloy probes were also tested for their effect on the same measurement parameters. Tests were also performed at probe loads from 10 to

45 gf to investigate effects due to probe load.

Tests of specimen preparation methods included alumina polishing and lapping

processes, but primary emphasis was placed on the use of various grades of

diamond (in the range 0.1- to S-ym particle size) for specimen polishing and

lapping. The reasons for this were twofold: 1 ) considerable experience in

the use of diamond for shallow angle sectioning of silicon specimens exists

in this laboratory; and 2) the use of diamond in oil, rather than aluminum

oxide in water, was expected to reduce the effect of° possible oxide formation

on the GaAs specimen surfaces.

Table 1 lists the specimens available for testing. The bulk p-type specimens

intended primarily for calibration were received toward the end of the project period and were not fully utilized. Table 2 lists the probes available

for the tests. The surface preparation media that were used are listed in

table 3. Because of the exploratory nature of this work, not all combinations of specimens, probes, surface preparations, and other operating conditions were tested. The primary emphasis was on identifying the measurement

conditions which yielded repeatable results consistent with the measurement

limitations of the instrumentation; those probes, probe loads, or surface

preparations which appeared to give only erratic results in the initial

phases were rejected in favor of more promising ones.

3.5 Experimental Results With Bulk GaAs

a) Effect of Probe Material and Probe Load

The first tests of measurement dependence on experimental conditions were

done on bulk (100) silicon-doped (approximately 7 x 10^^ cm”®) GaAs using a single tungsten-osmium probe. A large area tin-nickel, nickel, gold ohmic

contact (as described in sec. 2.2) was provided on the back surface of the

specimen, to complete the circuit. The response of the single probe was checked as a function of load (10, 20, 30, and 40 gf ) in both forward and

reverse bias on the as-received specimen surface. In forward bias, resistance increased with decreasing load while in reverse-bias no load dependence

15
Table 1. List of GaAs Specimens Available for Tests.

a. Bulk

Specimen ID

Conducti vi ty

Orientation Type Dopant

Carrier

Density (cm~^)

4481 (100) P zinc 4.5 X 10^6

3284 ( 1 00) P zinc 3.3 X 10^8

4464 (100) P zinc •

ID X O

»—

00

LI 723 (100) n silicon • o X 10l8

b. Ion Implanted

Specimen ID

Substrate

Orientation

and Type

Conductivity

Type of

Implanted

Layer

Implanted

Dopant

Implant

[ Fluence

(cm“^

)

Implant

Energy

(keV)

30-min

(°C)

LDB1 1 (100) — P

Be 5 X 10^^ 1 00 800

201 (100) n P

Be 5 X 10^^ 1 00 800

203 (100) SI* P

Be 5 X 10^^ 1 00 800

5-434 (110) — n Se

C\I

*-H X o 400 800

8163a (100) — n Si 5 X 10^2 1 70 800

8163b (100) — n Se 5 X 10^^ 300 850

* Semi -Insulating.

16
Table 2. Probes Available for Test

Probe Set Base Material Modifications, if any

1 tungsten osmium As purchased with commercial spreading resistance instrument

2 tungsten osmium Electroplated with rhodium

3 tungsten osmium Plated with indium-gallium paste

4 tungsten osmium Ion-implanted with indium at 200 keV

to a fluence of 1 x 10^^ cm~^ and

with gallium at 200 keV to a fluence

of 1 X 10^^ cm“^

5 tungsten osmium Implanted with gallium at 200 keV to

a fluence of 1 x 10^^ cm~^

6 tungsten ruthenium

7 tungsten carbide

Table 3. Surface Preparation Media Used.

a. Polishing

Medium Backing Material

colloidal silica

0.1 -ym diamond/oil

0.5-ym diamond/oil

0.3-ym alumina /water

1-ym diamond/oil

methyl methacrylate

ground glass

ground glass

glass

bonded to plastic tape

b. Lapping

6i-ym diamond/oil ground glass

17
was seen. While data taken under all conditions were quite repeatable, the

dynamic probe response curves, figure 7, showed that the probe did not attain

a stable reading within the measurement window of the data logging equipment.

The same general shape for the dynamic probe response was found in similar

tests with the remaining probe materials listed in table 2 in this singleprobe configuration, and for all probe materials in the two-probe configuration. It was also noted that for all types of probe material, contact resistance values on this specimen were noticeably larger than 10® and it thus

became necessary to find a means of lowering these values to the range acceptable for the instrumentation.

For this purpose, a microscope illuminator was used to enhance carrier injection in the area of the contacts for several types of probes. This procedure

did reduce the contact resistance by about an order of magnitude, but because

it caused a highly erratic dynamic probe response, this illumination procedure was deemed unsatisfactory.

Since the as-received surface on this specimen was not optimal for spreading

resistance measurements, further efforts to reduce the contact resistance

were concentrated on various specimen surface preparations. Also, since no improvement in terms of reduced contact resistance or better stability was found with any of the alternate probe types, most of the remaining work was done with tungsten-osmium probes. All tests below were done using the twoprobe configuration.

b) Effects of Specimen Surface Preparation

The effect of specimen surface preparation on measurement quality was initially tested on the same n~type (silicon-doped, about 7 x cm”®) GaAs

used above. Lapping with 6-ym diamond grit in oil on a frosted glass plate

gave a rough or matte surface finish similar to that typically obtained on silicon under the same conditions. Successive improvements in optical quality of the surface were obtained with 0.5- and 0.1 -ym diamond, respectively.

Figure 8 shows photomicrographs of typical "good" surfaces obtained with each

of the above procedures as well as a still more highly polished surface obtained by polishing against 1 -ym diamond bonded to plastic film.

It should be noted that it was much more difficult to obtain uniform and

reproducible surface quality on GaAs than on silicon with any of the polishing procedures tested. The most significant problem in this regard was

the tendency to develop areas of severe, deep scratches or "crumbling" of the

GaAs surface. This is illustrated in figure 9.

The measured two-probe resistance values from bulk n-type GaAs specimens

after polishing by the methods above did not show a linear correlation with

the visual surface quality of the various surfaces. Data taken either on the

matte surface (6-ym diamond lap) or on the reasonably well-polished surfaces

(0.1-ym diamond on ground glass or 1 -ym diamond on plastic tape) were of

nearly the same character as on the as-received specimen surface, having

average resistances above 10® Q, and a dynamic probe response which drifted

for the entire period of contact. However, data taken on the specimen polished with 0.5-ym diamond were noticeably improved; i.e., average resistance

18
MEASURED

RESISTANCE

(

flj

Figure 7. Dynamic probe response for six measurement cycles on silicon-doped

bulk GaAs as polished by the manufacturer.

19
Figure 8. Photomicrographs of typical good surfaces obtained on different

bulk GaAs specimens with four preparation procedures: (a) beveled against

ground glass with 6-ym diamond, (b) beveled against ground glass with O.S-ym

diamond, (c) beveled against ground glass with 0. 1 -urn diamond, (d) top surface polished with 1-ym diamond bonded to plastic tape. Parallel tracks in

the photomicrographs are damage marks left by the two probes (lateral separation = 60 um) during measurement.

20
a

Figure 9. Photomicrograph showing gross surface break-up or crumbling which

was sometimes encountered during beveling of GaAs specimens. Three regions

can be seen: (a) original top surface showing part of circular ohmic contact

(not used), (b) region of reasonable quality surface beveled using O.S-ym

diamond on ground glass, (c) region of severe surface crumbling. Once such

crumbling started, it was found to progress in the direction of the bevel

edge as more material was beveled away. Lateral separation of probe tracks

seen in region (b) is 60 pm.

21
was decreased by a factor of nearly four, and nearly complete stabilization

of the dynamic probe response was obtained within the measurement window,

A direct comparison of two surface finishes and the resulting resistance

measurements is given in figure 10. This figure shows surface morphology of

a specimen polished at a shallow angle with O.S-ym diamond on frosted glass

subsequent to top-surface polishing with 1 -ym diamond bonded to plastic tape,

and also some two-probe resistance data from each surface. (The dynamic

probe response on the surface polished with 0.5-ym diamond was very similar

to that shown for silicon in fig. 6. ) This observed dependence of spreading

resistance on surface finish does not appear to parallel that found by

Queirolo [19] for n-type GaAs, However, it does indicate that at least one diamond-polished surface preparation allows data to be acquired within the

10® Q. maximum resistance limit of the instrumentation for n-type GaAs specimens doped in the low- or mid-10^^ cm“® range. Further, this preparation,

polishing with 0.5-ym diamond, is generally compatible with the shallow angle

sectioning necessary for profiling implanted layers.

3.6 Experimental Results With Implanted Layers in GaAs

a) Beryllium (p-Type) Layer Profile Data

Initial tests of implanted layer profiling were done on specimens implanted

with beryllium. The same lowering of contact resistance after 0.5-ym diamond

polishing, previously seen for bulk n-type GaAs, was also seen for these

p-type layers. Figure 11 shows the condition of the specimen surface and

profile data following beveling with 0.5-ym diamond and with 0. 1 -ym diamond

(both against lapped glass). Figure 12 shows the- repeatability of the measurement for four more runs taken on another chip of the same specimen freshly bevel-polished with 0.5-ym diamond. The dynamic probe response data which

were taken along with several of these runs showed an unexpected result: the

contacts do not really stabilize on the more heavily doped region of the

implanted layer, yet they stabilize rather well in the lightly doped deeperlying region. The mechanism for this effect and its dependence on specimen

preparation damage are not known. However, the presence of this effect suggests that the profile data from different regions of the implant may have

different reliability. Profile data and dynamic probe response traces were taken on this specimen at probe loads of 20, 30 and 40 grams. No significant

dependence of absolute resistance values or character of the dynamic probe

response upon probe load was seen. Samples from a second specimen implanted

with beryllium under the same implantation conditions and having the same anneal cycle as the first gave two-probe resistance profile data almost identical to that of the first specimen.

b) Calibration of Implanted Layer Profile

An estimate of peak beryllium implant density was obtained by calibrating the

probes against three bulk specimens of GaAs doped p-type with zinc. Because

of the limited resolution imposed by the measurement repeatability and by the

small number of calibration specimens, the dopant density for the bulk calibration specimens was taken from the vendor's Hall effect measurements on adjacent, or nearly adjacent, slices from each of the crystals. These specimens were polished using 0.5-ym diamond on glass so that the surface prepara22
I U I 33NViSIS3il a3»nSV3M

23

Figure

10.

Surface

finish

and

spreading

resistance

data

for

silicon-doped

bulk

GaAs

specimen

which

had

been

top-surface

polished

with

l-pm

diamond

bonded

by

plastic

tape

and

then

beveled

with

0.

5-pm

diamond

against

ground

glass;

(a)

photomicrograph

of

specimen;

the

portion

polished

with

0.5-iim

diamond

on

glass

is

seen

at

left

of

picture;

(b)

spreading

resistance

data

taken

on

both

surfaces.

Probe

step

increment

for

tracks

seen

in

figure

10a
a

LUO

00

00

LU

00

DEPTH (yum)

c d

Figure 11. Specimen surface finish and profile data for beryllium-implanted

GaAs which has been beveled by two different procedures: (a) and (c) 0.5-iJm

diamond against lapped glass, (b) and (d) 0.1 -pm diamond against lapped

glass. Lateral separation of probe tracks in (a) and (b) is 60 ym.

24
MEASURED

RESISTANCE

f

II

I

DEPTH

e

*

Figure 12. Four sets of spreading resistance depth profile measurement on beryllium-implanted GaAs showing repeatability generally obtained on a specimen beveled with 0.5-ym diamond.

25

•

•,
tion would be the same as that on the implanted specimens. The calibration

relation was established by piecewise straight-line fitting on a log-log

scale of adjacent pairs of two-probe resistance data (from the calibration

specimens) to the inverses of the dopant density values for these specimens.

The dopant density profile of the ion-implanted layer is then obtained from

direct interpolation of its measured resistance values on the calibration

scale to obtain dopant density values. No spreading resistance sampling

volume correction is applied to the test specimen profile data since, for the

reasons stated in section 3.2, the spreading resistance is only a very small

component of the measured two-probe resistance values.

Based on the two-probe resistance measurements on these specimens at 30 gf,

the peak beryllium density (for profile data taken several weeks prior to

arrival of the bulk n-type calibration specimens) was estimated to be between

2 X 10-^ and 5 x 10-^' cm“^ for most measurement sets. This value is noticeably lower than reported by McLevidge [18] for a beryllium layer implanted

under identical conditions but annealed at 900°C for 30 min (instead of 800°C

for 30 min as used for the present work). However, figure 13 shows a profile

indicating noticeably higher dopant density values obtained on one of the

beryllium-implanted specimens when it was prepared and measured sequentially

with the calibration specimens. The difference in peak beryllium density

between the earlier profiles (not shown) and that shown in figure 13 may be

due to changes in the probe's calibration response during the several weeks

intervening. Nevertheless, reasonable profiles of beryllium-implanted layers

appear to be obtainable.

c) Anomalous Differences in Sensitivity to Probe Force_

Auxiliary tests on the bulk p-type calibration specimens show that a significant dependence of spreading resistance upon probe force exists for the two more heavily doped specimens, and a moderate probe force dependence exists

for the more lightly doped specimen. These probe force dependences were

found to exist to about the same extent following beveling of the bulk specimens with either 1- or 0, 1 -ym diamond or with 3-um alumina. This result is

similar to results obtained on the bulk n-type specimens (sec. 3.5a). However, it is inconsistent with results obtained on the p-type implanted layers

on which no probe force dependence was found. It does indicate, however,

that the resultant dopant profile of a p-type implanted layer may well depend

on probe force, since the calibration scale derived from measurements on bulk

GaAs was found to depend on probe force.

d) Silicon and Selenium (n-Type) Layer Profile Data

Efforts to profile silicon- and selenium-implanted layers (n-type) in GaAs

were, in general, less successful. This was due in part to the inability to

find a surface preparation which would adequately reduce the contact resistance of n-type layers significantly below the 10® upper limit of the instrumentation. Based on initial tests on the bulk n-type specimen, even the

best surface preparation tested, 0.5-um diamond polishing, would only allow

measurement of dopant density above about 3 x lO-*- cm~^ . Since two of the

three available n-type implanted layers were implanted at relatively low

fluences, emphasis was placed on the remaining specimen. This specimen was

26
DOPANT

DENSITY

|cm'^

)

Figure 13. Dopant density depth profile for a beryllium-implanted GaAs specimen beveled with 0. 5-ym diamond against ground glass. The apparatus was calibrated using three zinc-doped GaAs bulk specimens beveled in the same

manner.

27
implanted with selenium at a fluence of 5 x 10^“^ cm~^ and was expected from

projected range statistics [19] to have a peak dopant density nearly

2 X 10-^^ cm~'^, well in excess of the minimum detectable level estimated

above, (Not all of these dopant atoms may have been activated during the

anneal cycle, however. ) For reference, the predicted dopant profile for this

layer, based on the theoretical work of Winterbon [20] is shown in figure 14;

the profile of the low-fluence (5 x io^^ cm“^ ) silicon implant similarly

calculated is shown in figure 15.

Based on the resistance profile data from the beryllium-implanted layers, it was expected that the resistance profile of the selenium implant would also

be similar in shape to the inverse of the dopant profile (fig. 14). Further,

based on the resistance values measured on the bulk n-type specimen (sec.

3.5) and the estimated peak dopant density of the selenium layer, it was expected that the selenium layer would have a minimum value in its resistance

profile between 10^ and 10^ fl. Finally, based on the dopant distribution

shown in figure 14, all structure in the resistance profile due to the implanted layer should occur within less than 0.3 ym; resistance values should

increase to values typical of the substrate, 10® or higher, by the end of

this depth range. Based on these expectations, no sign of the implanted

layer character is seen in the resistance profile data of figure 16a. The

shape of the resistance profile data for this specimen changed only marginally despite repeated beveling and remeasurement, including use of various

other polishing media and lighter mounting fixtures to reduce damage during

beveling.

As further evidence that the small change in resistance values shown in figure 16a is not due to the heavy dose selenium implant, profile data were

taken on a silicon layer, figure 16b, implanted at a fluence nearly two orders of magnitude lower than the selenium layer. This specimen was expected

to have a peak dopant density (fig. 15) nearly two orders of magnitude less

than that of the selenium implant (fig. 14). Nevertheless, its resistance

profile has nearly the same shape and absolute values as that of the selenium

layer. These data apparently indicate that for n-type implants, the twoprobe resistance values are more controlled by mechanisms, possibly lattice

damage or surface states, that are not proportional to the dopant density.

3.7 Summary

Spreading resistance measurements on GaAs are very sensitive to surface preparation. This was demonstrated by Queirolo and supported here for different

types of preparation; however, the two sets of results are not fully consistent in their particulars. Also, reproducibility of surface quality and of

measurement quality, even for a fixed type of preparation, is poorer for GaAs

than for silicon. Excess damage and deep scratches, which are atypical of

the finish normally produced by a given polishing medium on silicon, occur readily in GaAs and great care must be taken during polishing. Further,

Queirolo has stated that changes of the entire calibration curve, by a factor

as large as five, have been experienced for a fixed set of probes and a fixed

preparation procedure [21].

A nonaqueous specimen surface preparation, polishing with 0.5-Mm diamond in

oil, was found to give acceptably low resistance values on bulk n- and p-type

28
DOPANT

DENSITY

fcm-3|

Figure 14. Dopant density profile predicted according to the procedure of

Winterbon [20] for the seleniiim-implanted layer shown in figure 16a. This

profile illustrates location of peak density (minimum resistance) and total

depth scale expected in data of figure 16a.

29
DOPANT

DENSITY

Icm'^)

0.00 0.10 0.20 0.30 0.40 0.50

DEPTH (Mtn|

Figure 15. Dopant density profile predicted according to the procedure of

Winterbon [20] for the silicon-implanted layer shown in figure 16b. This

profile illustrates the location of peak density (minimum resistance) and

total depth scale expected in data of figure 16b.

30
MEASURED

RESISTANCE

(H

|

DEPTH l/um) DEPTH (mhi)

a b

Figure 16. Two-probe resistance profile data for (a) selenium layer implanted into GaAs at 300 keV with a fluence of 5 x 10^^ cm~^ , and (b) silicon

layer implanted into GaAs at 170 keV with a fluence of 5 x 10^^ cm~^.

31
specimens for measurement with commercial spreading resistance equipment.

The resistance values obtained with this preparation on the bulk n-type specimen reported in section 3.5 were slightly lower than obtained by Queirolo

for a comparably doped specimen prepared with alumina in water. However,

values obtained after polishing bulk p-type specimens with O.S-pm diamond

were somewhat higher than those reported by Queirolo for alumina polished ptype bulk specimens. Application of 0.5-ym diamond polishing to implanted

specimens showed that measurements on implanted layers of either conductivity

type are much less sensitive to probe force than are measurements on comparably polished bulk specimens.

With respect to implanted layers, additional improvement can probably be

expected with more extensive testing and refining of surface preparation

techniques to reduce residual damage. At present, it is probably desirable

to mount calibration chips on the same block as the specimen chip to be sec- tioned for profiling to attempt to maintain the same surface quality for each

piece. The inability to profile n-type implanted layers is not understood.

The similarity of measurement results on two n-type implanted layers with

widely different dopant densities and the difference between measurement

results on these layers and on n-type bulk suggest that the measurement is

controlled by the specimen through surface states or damage mechanisms rather

than by the probes.

3.8 Recommendation

It appears desirable in any future development of the two-probe spreading

resistance technique for application to GaAs to place emphasis on the testing

of and the development of an understanding of the parameters which control

contact resistance (absolute levels and reproducibility of values) for point

pressure contacts. In particular, two questions raised in the present investigation need more detailed study and understanding. The first is the apparent difference in the way specimen preparation damage interacts with thin n- type layers compared with bulk specimens of either conductivity or with thin

p-type layers. This question was raised by the inability to obtain satisfactorily low-resistance values on the high fluence n-type implants. The existence of a similar measurement problem should be looked for on n-type diffused and epitaxial layers. These layers are free from concerns over the

fraction of dopant activated and from the damage due to fabrication encountered in implanted specimens. The second question relates to the observed

difference in probe-force dependence of measured resistance between bulk and

thin graded-layer specimens. This difference has great importance for establishing a proper calibration procedure. The possible lack of probe force

dependence on all graded layers should likewise be examined on diffused layers to aid in understanding how such an effect may be controlled by dopant

profile gradient or intrinsic unannealed damage due to implantation. Once

such questions are resolved for relatively thick diffused and epitaxial layers, a more reasonable choice of operating conditions can be made for improving the ability to profile thin implanted layers. Beveling techniques such

as the use of chemical or chem-mechanical procedures to minimize induced

damage and further alternate probe alloys to reduce contact resistance may

also require further investigation.

32
REFERENCES

1. Aven, M. , and Swank, R. K. , Ohmic Contacts to Wide Band Gap Semiconductors, Ohmia Contacts to Serrriaonduotovs (Electrochemical Society, Inc.,

1969), pp. 69-81.

2. Van Laar, J. , and Scheer, J. J. , Influence of Volume Dope on Fermi Level

Position at Gallium Arsenide Surfaces, Surface Science _8, 342-356 (1967).

3. See, for example, Sze, s. M. , Physics of Semiconductor Devices (wileyInterscience, New York, N.Y. , 1969), p. 369.

4. Mead, C. A., and Spitzer, W, G. , Fermi Position at Metal-Semiconductor

Interfaces, Phys, Rev, _1_^, A713-A716 (1964).

5. Gregory, P. E. , Spicer, W. E. , Ciraci, S., and Harrison, W. A., Surface

State Band on GaAs (100) Face, Appt, Phys. Lett, 2^, 511-514 (1974).

6. Spicer, W. E. , Chye, P. W. , Skeath, P. R. , Su, C.Y. , and Lindau, I., New

and Unified Model for Schottky Barrier and III-V Insulator Interface

States Formation, J, Vac, Sci, Technol, J_6, 1422-1432 ( 1979).

7. Mattauch, R. J. , and Green, G. , private communication, 1979.

8. Wolfstirn, K. B. , and Focht, M, W. , Thermoelectric n-p Tester Using ac Bias for Gallium Arsenide and Gallium Phosphide, Rev, Sci. Instrum, 42 , 152-154 (1971).

9. Neumark, G. F. , Fitzpatrick, B. J. , Harnack, P. M. , Herko, S. P. , Kosai,

K. , and Bhargava, R. N. , Potential Profiling as a Means to Determine

Conductivity Type: Application to ZnSe , J, Etectrochem. Soc, 127 , 983-

985 (1980).

10. Oettinger, F. F. , and Larrabee, R. D. , Eds., Measurement Techniques for

High Power Semiconductor Materials and Devices: Annual Report, October

I, 1978 to September 30, 1979, NBSIR 80-2061 (August 1980).

11. McCombe, B. D. , Characterization of III-V Materials, Naval Research

Laboratory, NRL Memorandum Report 3701 (February 1978).

12. Frank, H. , and Azim, S. A., Measurement of Diffusion Profiles of Zn in

N-Type GaAs by a Spreading Resistance Technique, Solid State Electronics 727-728 (1967).

13. Goodfellow, R. C. , Carter, A. C. , Davis, R. , and Hill, C. , New Contact

Resistance Profiling Method for the Assessment of III-V Alloy Multilayer

Structures, Electron. Lett. J_4, 328-330 (1978).

14. Queirolo, G. , Spreading Resistance Measurements on Gallium Arsenide,

J. Electrochem, Soc. i 25 , 1627-1676 (1978).

15. Solid State Measurements, 600 Seco Rd. , Monroeville, Pennsylvania.

33
16. Schumann, P. A., and Gardner, E, E. , Spreading Resistance Correction

Factors, Solid State Eleatvonias _1_2, 371-375 ( 1969).

17. Dickey, D. H. , and Ehrstein, J. R. , Semieonduator Measurement Technology: Spreading Resistance Analysis for Silicon Layers with Nonuniform

Resistivity, NBS Spec. Publ. 400-48 (May 1978).

18. McLevidge, W. V., Annealing Studies of Beryllium in Gallium Arsenide and

Gallium Arsenide Phosphide, Report R-802, Coordinated Science Laboratory

University of Illinois, Urbana, Illinois (December 1977).

19. Gibbons, J. F. , Johnson, W. F. , and Mylroie, S. W. , Projected Range

Statistics, Semiconductors and Related Materials^ 2nd ed. (Dowden,

Hutchinson and Ross Inc., 1975, distributed by Halstead Press).

20. Winterbon, K. B. , Computing Moments of Implanted-Ion Range and Energy

Distributions, Report AECL 5536, Chalk River Nuclear Laboratories, Chalk

River, Ontario (June 1976).

21. Queirolo, G. , private communication.

34
NBS»n4A (REV. 2»8C) U.S. DEPT. OF COMM.

BIBLIOGRAPHIC DATA

SHEET (See /n struct/ons^

4. TITLE AND SUBTITLE

PUBLICATION OR

REPORT NO.

NBSIR 81-2403

2. Performing Organ. Report NoJ 3. Publication Date December 1981

Gallium Arsenide Materials Characterization:

Annual Report, October 12, 1978 to October 12, 1979

5. AUTHOR(S)

J. R. Ehrstein and A. C. Seabaugh

6. PERFORMING ORGANIZATION (If joint or other than NBS, see instructions) 7. Contract/Grant No.

national bureau of standards

DEPARTMENT OF COMMERCE

WASHINGTON, O.C. 20234

8 . Type of Report & Period Covered

Final, 10/12/78 to

10/12/79

9. SPONSORING ORGANIZATION NAME AND COMPLETE ADDRESS (Street. City. State. ZIP)

Department of the Army

U.S. Army Electronics Technology and Devices Laboratory

Fort Monmouth, NJ 07703

10.

SUPPLEMENTARY NOTES

I I Document describes a computer program; SF-185, FIPS Software Summary, is attached.

11.

ABSTRACT (A 200-word or less factual summary of most significant information. If document includes a significant

bibliography or literature survey, mention it here)

Ohmic and Schottky barrier contacts for use in electrical characterization were examined both conceptually' and experimentally with particular focus on the problems

associated with ohmic contacts to semi-insulating GaAs. The conductivity type of

the semi-insulating material, which can be either n- or p-type, was investigated by

means of a potential profiling technique. In addition, the feasibility of spreading

resistance measurements was examined and applied to both low resistivity bulk GaAs

and ion-implanted semi-insulating substrate material.

12.

KEY WORDS (Six to twelve entries; alphabetical order; capitalize only proper names; and separate key words by semicolons)

Contacts; gallium arsenide; potential profiling; spreading resistance.

13. AVAILABILITY 14. NO. OF

PRINTED PAGES

1 X i Unlimited

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1 1 Order From Superintendent of Documents, U.S. Government Printing Office, Washington, D.C. 38

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