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Submitted on 1 Jan 1975
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Resistivity annealing properties of aluminium thin films
after ion implantation at liquid helium temperatures
A.M. Lamoise, J. Chaumont, Frédéric Meunier, H. Bernas
To cite this version:
RESISTIVITY
ANNEALING
PROPERTIES
OF ALUMINIUM THIN
FILMS
AFTER ION
IMPLANTATION
AT
LIQUID
HELIUM
TEMPERATURES
(*)
A. M. LAMOISE and J. CHAUMONT
Laboratoire René Bernas du
Centre de
Spectrométrie
Nucléaire etSpectrométrie
deMasse,
91406
Orsay,
FranceF. MEUNIER
Laboratoire de
Physique
des Solides(**)
UniversitéParis-Sud,
91406Orsay,
FranceH. BERNAS
Institut de
Physique
Nucléaire,
UniversitéParis-Sud,
91406Orsay,
France(Re~u
le9 juillet
1975,
accepte
le 26septembre
1975)
Résumé. 2014 Nous
présentons les
premiers
résultats de recuit de résistivité pour des couches minces d’aluminiumaprès
implantation d’ions Al, H et O à des températures inférieures à 6 K. La courbe de recuit aprèsimplantation
d’ions Al est semblable à celle obtenueaprès
irradiation aux neutrons.L’implantation d’ions H à faible dose fait
apparaitre
deux pics très marqués au stade I du recuit.Après
implantation de fortes doses d’hydrogène, la courbe de recuit indique lapossibilité
d’un ordre des ions H ou bien d’une transformation de phase.Abstract. 2014 We
present the first resistivity annealing curves of Al after
implantation
of Al-, H-,and O-ions at liquid helium temperatures. The Al-implantation produces a curve resembling that
of neutron-irradiated Al ; low-dose H-
implantation
results in two strongly enhanced stage I recoverypeaks, while high-dose H-
implantation
annealing results suggest that H-ordering or a phase trans-formation takesplace.
Classification
Physics Abstracts
7.188 - 8.362
Although
ionimplantation
in metals is awell-developed technique
[1],
the standardtechniques
of radiationdamage physics
have not yet all found theirapplication
in this field. This is of course due to therelatively
lowimplantation energies : typical
rangeprofiles
rarely
gobeyond ~
1 000A
so thatsamples
must be made of thin films in order to use
techniques
such as
resistivity
measurements with a reasonablesignal-to-noise
ratio.Moreover,
it is often necessaryto
operate
at lowtemperatures
andimplantation
conditions are ingeneral
rather unfavourable forsuch
experiments.
Anotherprejudice against
resis-tivity
measurements onimplanted
metal thin filmswas that since the film thickness is of the order of the
conduction electron mean free
path,
theresistivity
change
due to radiation-induced defectannealing
would be washed outby
the size effect of the film.We have set up a
liquid
He cryostat on theOrsay
ionimplantor,
and haveequipped
it so thatreasonably
accurate
resistivity
annealing
experiments
can becarried out on
implanted
metallic thin films. In thispaper, we
present
our first results onion-implanted
Alfilms. In order to determine the effect of ion-induced radiation
damage alone,
Al wasimplanted
into Al atfairly
low doses. H-implanted
Al(again
at lowdose)
provided
information on theannealing
spectrum
of interstitials. Because of their
interesting
super-conducting
properties [2]
theresistivity annealing
of the concentrated Al-H systems was also measured.Finally,
in a search for chemicaleffects
related tooxide
formation,
we have studied theresistivity
annealing
of concentrated 0-implanted
Al. The results on the varioussamples
arestrikingly
different,
and indicate that
resistivity annealing experiments
can
be,
quite
useful inunderstanding
theproperties
of
implanted
metals andalloys.
The
experimental
arrangement and filmpreparation
L-306 JOURNAL DE PHYSIQUE - LETTRES
technique
arebriefly
summarized in[2],
and will be described in detail elsewhere. The aluminium films(typically
10 x 0.3mm2,
thickness 1 300-1 650A)
were
prepared
by
Alevaporation
oncrystalline
quartz
substrates in a standardbell-jar
vacuum.Their
resistivity
ratiop(300
K)/p(4.2
K)
was about 2.7.Resistivities were measured
using
a standardfour-point probe
technique,
and size andimpurity
effectswere normalized out
by
simultaneous measurement of theimplanted sample
and of an identical film mountedin the cryostat at the same
time,
but shielded from theion beam. Al-
implantation
was carried out at asingle
energy(100
keV-Al).
Using
standardslowing-down
theory [3],
the range and range distribution areestimated at 1 200
A
and 400A,
respectively.
For the 1 500A -
thick film used in this case, thisproduces
a
sample
which has beenimplanted throughout.
The measured
resistivity
is of course an average, sincethe defect
depth
distribution isapproximately
gaus-sian. We also find that theresistivity
increase is notproportional
to the dose.Although
thisprevents
precise
absolute measurements, it still allows better thanorder-of-magnitude
values of the radiation inducedresistivity
increment to beobtained,
as wellas accurate relative
resistivity annealing
measure-ments. For thelightest
ions(especially
H andD),
the rangeparameters
aresubject
tolarger
uncertaintiesand
the range distributions arerelatively
narrower[4].
Hence
(i)
in order to obtain moreuniform samples,
two or threeimplantations
(at
differentenergies)
had to be carried out, and
(ii)
anapproximate
total absoluteresistivity
increase was deduced from thevalues measured after the last of the successive
implan-tations. For
example,
in the case of atypical
H-implantation
the measured film resistance increased from 1.53 Q to 19.30 Q after a 10keV/amu
implanta-tion at a dose of
1018
at . cm - 2,
then to 31.5 Qafter a 5
keV/amu implantation
at a dose of 7 x1017
at. cm -2,
andfinally
to 38.7 Q aftera 2.5
keV/amu implantation
at a dose of1017 at . cm - 2
( 1 ).
(Dose
ratesranged
from 8 x1015 at. cm - 2 . S - 1
to 2 x1015
at CM-2.S-1.)
The
resistivity annealing
curve obtained onAl-implanted
Al at arelatively
low dose ispresented
infigure
la andcompared
to the resultpreviously
obtainedby Burger et
al.[5]
on neutron-irradiatedbulk Al. It is
readily
seen that thegeneral shape
ofthe
annealing
spectra
arequite
similar. Theannealing
peaks
at 19 K(usually
ascribed toclose-pair annealing)
and - 230 K
(stage III)
are absent in theion-implant-ed
sample,
while the detailed structure of stage IIannealing
differs somewhat. The overallsimilarity
is
comforting,
as neutron- and ion- irradiation areexpected
toproduce
similardamage :
this indicates that film size effects do not dominate theannealing
process, apoint
that is reinforcedby
the fact that thee) These values may be accounted for if the tail of the implan-tation profile extends out to the surface.
FIG. 1. - a) Differential resistivity annealing curve for
Al-implanted Al, at a dose of 3 x 1013 at . cm- 2 (dose rate of 8 x 1014 at. cm - 2 . S - 1). The film resistivity was ~ 5 ~,~ . cm
before implantation and 7.5 Jl!1. cm after implantation. b) Diffe-rential resistivity annealing curve for neutron-irradiated bulk Al
according to reference [5].
same
annealing
spectrum
was found after Al-implan-tation in a 450
A -
thick film. The absence of thepeak
at 230 K mayyield
some information on thpconcentration of energy
deposition (hence
of defectcreation)
due to theincoming
ion : if thedamage
are more
probable
’than monovacancyformation,
a process that would lead to a strongerannealing
in the firstpart
of stage III(if
one assumes that all ofstage
III is due to vacancyannealing).
The dosedependence
of the relativeresistivity
increase is shown infigure
2 : the incrementalchange
in theresistivity
shows an inverse-dosedependence
overnearly
three orders ofmagnitude.
FIG. 2. - Dose
dependence of relative resistivity increment for
Al-implanted Al (implantation energy 100 keV ; film thickness 1300
A).
The effect of interstitial
hydrogen
isstrikingly
demonstrated infigure 3a ;
whencompared
tofigure
laa two-fold increase is found in
stage
Iannealing
andthe stage III
annealing amplitude
iscorrespondingly
reduced. The reappearance of alarge close-pair
annealing
peak
at 19 K can be accounted forby
thelower
deposited
energy concentrationproduced
by
H-
implantation.
Athigh, fairly uniform
concentra-tions,
theannealing
spectrum shiftsconsiderably
towardhigher energies.
We have made noattempt
to
interpret
the observedpeaks,
but it isquite
clear that at least some of them(see
dottedpeak
at 200 Kin
figure
3b andpeak
at 300 K infigure 3c)
are far toosharp
to be accounted forby
themigration
of asimple
defect : H-
disordering and/or phase
transformations couldpossibly
occur,accompanied
or followedby
bubble formation as evidenced
by
optical microscopy
onroom-temperature
annealedsamples.
The
annealing
spectrum
ofhigh-dose
0-implanted
Al(Fig.
4)
isagain quite
different. The results are toopreliminary
to allow anyanalysis,
butthey
do suggestthat
resistivity annealing
experiments
may be aninteresting
method for thestudy
of oxide formation after lowtemperature
implantation.
Further work isobviously
needed to obtainquantitative
information,
but a number ofinteresting
features havealready
appeared
in thesepreliminary resistivity annealing
experiments
onlow-temperature implanted
films.FIG. 3. - Differential
resistivity annealing curves for H- implanted
AI at : a) low dose, for which a 15 keV/amu implantation
produced
the same total resistivity change as Al in figure I a) ; b) high total dose and fairly uniform concentration obtained by implanting
at 10, 5 and 2.5 keV/amu; c) same as b) with concentration
multi-plied by 10. Dose rates ranged from 8 x IOt5 at.cm-2-s-1 to
2 x 1015 at . cm-2 . s-1. Note : Due to temperature limitations, curve b) could not be followed above 330 K. However, at that
"
L-308 JOURNAL DE PHYSIQUE - LETTRES
Acknowledgments.
- We wish toacknowledge
Dr. P. Lucasson for useful discussions and F. Lalu and M. Salome as well as S. Buhler and the
Low-Temperature Group
of Institut dePhysique
Nucleaire,
Orsay,
for theirhelp
indesigning,
building
andoperat-ing
the cryostat.FIG. 4. - Differential
resistivity annealing curve for 0- implanted
Al at high, fairly uniform concentration (implantation energies 50 and 25 keV/amu). See note in figure 3. In this case, - 70 % of the
resistivity increase remains at 330 K.
References
[1] Ion Implantation in Metals, ed. S. T. Picraux, E. P. Eer Nisse and F. Vook (Plenum Press, N. Y.) 1974.
[2] LAMOISE, A. M., CHAUMONT, J., MEUNIER, F. and BERNAS, H.,
to be published.
[3] LINDHARD, J., SCHARFF, M. and SCHIØTT, H., Mat. Fys. Medd.
Dan. Vid. Selsk. 33 (1963) 14.
[4] SCHIØTT, H., Mat. Fys. Medd. Dan. Vid. Selsk. 35 (1966) 9.
[5] BURGER, G., ISEBECK, K., VÖLKL, J., SCHILLING, W. and WENZL,
H., Z. Angew. Phys. 22 (1967) 452.
[6] CORBETT, J. W., SMITH, R. B. and WALKER, R. M., Phys. Rev.