Growth of Ag films on polyethylene terephthalate (PET) deposited by electron beam
Transcript of Growth of Ag films on polyethylene terephthalate (PET) deposited by electron beam
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Thin Solid Films 495 (
Growth of Ag films on polyethylene terephthalate (PET) deposited
by electron beam
I. Prosy*evas a, J. Puixo a,b,*, S. Tamulevi*ius a,b, A. Juraitis a, M. Andrulevi*ius a, B Cy”iute b
a Institute of Physical Electronics, Kaunas University of Technology, Savanoriu 271, LT-50131, Kaunas, Lithuaniab Department of Physics, Kaunas University of Technology, Studentu 50, LT- 51368, Kaunas, Lithuania
Available online 30 September 2005
Abstract
The optical and structural properties of silver (semi-continuous and continuous) layers on optical polymer (PET) deposited by electron beam
evaporation were investigated at different growth stages. The experimental results have shown that thermal annealing of discontinuous silver
layers at temperatures close to the polymer glassing temperatures brings to formation of nanostructured interface.
D 2005 Elsevier B.V. All rights reserved.
Keywords: Polyethylene terephthalate; Electron beam evaporation; Nanostructures; Glassing temperature; Ag films
1. Introduction
Metallization of polymers is essential for realizing their
application in elements of microelectronics, photonics devices,
biosensors and medical implants [1–16]. The main reason of
interesting in polymer metallization is the low-cost and high-
performance polymer electronic devices, a very low absorption
in the visible wavelength range [14]. Outstanding properties of
polymer webs compared to glass substrates are their lightweight
and their flexibility, thus they are used especially on curved
surfaces and in portable electronic devices [4,5,12]. The
adhesion between metals and polymers is normally very poor.
The cohesive energy of not too reactive metals is typically two
orders of magnitude higher than that of polymers. Furthermore,
the interaction between moderately reactive metals and poly-
mers is generally very weak in comparison to the strong metal–
metal-binding forces. As a consequence, these metals are
expected to exhibit a strong aggregation tendency, and their
solubility in polymers should be extremely low under equilib-
rium conditions. The polymer surfaces are usually non-polar or
have very low wettability. For the same reasons metals of low
reactivity do not wet untreated polymer surfaces. They form
0040-6090/$ - see front matter D 2005 Elsevier B.V. All rights reserved.
doi:10.1016/j.tsf.2005.08.278
* Corresponding author. Department of Physics, Kaunas University of
Technology, Studentu 50, LT- 51368, Kaunas, Lithuania. Tel.: +37037
313432; fax: +37037 314432.
E-mail address: [email protected] (J. Puixo).
3D-clusters during vacuum deposition, which finally coalesce,
and form a continuous film at high metal coverage [1–10].
Usually metals are deposited on top of polymer films by thermal
evaporation under a high vacuum condition. The metal atoms
can readily diffuse in to the top surface region of the polymer
film and form a diffuse interface of several nanometers with a
depth distribution of metal atoms [9]. Sometimes metal atoms
react with the polymer and produce nanocomposites [3,9].
The use of a polyethylene terephthalate (PET) web as an
optical polymer substrate for the deposition of silver layer
stacks has various application advantages: high melting
temperature, good mechanical properties and recyclablity [3].
Optical properties of Ag polymer system can be affected by
film thickness and deposition parameters for the Ag film [13].
The quality of the interfaces between the silver layer and PET,
when the deposition temperature is close to PET glassing
temperature is a key factor in the manufacturing of induced
transmittance filters and mirrors.
This paper presents the research on Ag-PET system
produced by electron beam evaporation concentrating on the
mechanism of interface formation at temperatures close to the
PET glassing temperature.
2. Experimental
Substrates PET (polyethylene terephthalate, 25 Am) were
metallized with silver Ag (Tmelting=961.93-C) (purity 99,99%,
2006) 118 – 123
ww
40 50 60 70 80 90 100400
600
800
1000
1200
PET
PETAgc(111)
2ΘIn
tens
ity
(a.u
.)
20 nm on PET as-deposited
20 nm on PET after annealing at 1400C in air PET
a
40 50 60 70 80 90 1000
500
1000
1500
2000
2500
3000
3500
4000
4500
Ag2Oh (003)
Agc(311)
Agc(200)
Agc(222)
PET
Agc(111)
Inte
nsit
y (a
.u.)
100 nm on PET
100 nm on PET annealing at 1400C in air
PET
c
40 50 60 70 80 90 100400
600
800
1000
1200
Agc(311)
Agc(200)
PET
PET
Agc(111)
2Θ
2Θ
Inte
nsit
y (a
.u.)
50 nm on PET as-deposited
50 nm on PET after annealing at 1400C in air PET
b
Fig. 1. XRD pattern of Ag films on PET substrate of different thickness as
deposited and under annealing for 30 min at 140 -C. a) 20 nm, b) 50 nm, c)
100 nm.
I. Prosycevas et al. / Thin Solid Films 495 (2006) 118–123 119
Sigma Aldrich, UK) of different thickness: 20 nm, 50 nm, 100
nm by electron beam evaporation (Tsubstrate=80 -C, residualgas pressure 10�4 Pa, deposition rate v=1–2 nm/s). Before
coating substrates were cleaned using oxygen plasma proces-
sing (RF=13.56 MHz, P=0.3 W/cm2, t=5–60 s) [17]. The
contact angle of water on polymer substrate was measured by
self-made contact angle analyzer [17]. The film thickness
during deposition was monitored with a quartz balance
technique. The temperature of the substrates during deposition
was controlled with a precision T0.5 -C. After thin film
deposition part of Ag-PET structures were thermally annealed
at 140 -C for 30 min. The X-ray diffraction measurements for
the as-deposited as well as-annealed films were recorded at
room temperature in a DRON-3.0 diffractometer using Ni-
filtered CuKa radiation operating at 30 kV and 30 mA in a step
scan mode with a step size of 0.02-, for 2h and registration
time of 20s per step. XRD analysis of Ag films on PET was
performed to define values of interplanar distance d111, lattice
constant as well as grain size and microstrain. Winfit!1.2
software was used in these calculations [18]. Atomic force
microscope NANOTOP-206 operating in a contact mode
(cantilever force constant 0.9 N/m) was used to investigate
morphology of the surface. Image processing and analysis of
scanning probe microscopy data was performed using a
Windows-based program ‘‘Surface View version 5.0’’. Statis-
tical evaluation of the surface morphology was performed for
the scanning area 13 Am�13 Am. The optical transmittance
and reflection of the films were measured by the spectrometer
UV-VIS Specord in the 300–800 nm wavelength ranges. The
composition and chemical state of the elements in the silver
film surface were studied by X-ray Photoelectron Spectroscopy
(XPS) on KRATOS ANALYTICAL XSAM800. The energy
scale of the spectrometer was calibrated using Au 4f7/2 and Cu
2p3/2 Ag 3d5/2 peaks, [19]. The source was operating in
aluminum anode mode: Al Ka with photon energy of 1486.6
eV. The hemispherical analyzer with pass energy of 20 eV (0.1
eV energy increment) and fixed analyzer transmission (FAT)
mode were used. Carbon, oxygen and silver relative atomic
concentrations were calculated from appropriate peak area with
respect to the sensitivity factors, using original KRATOS
software. The ‘‘XPSPEAK41’’ software was employed for the
peak fitting procedure. The Shirley background with Lorenz to
Gauss rate 40:60 and asymmetric line shape (asymmetry
parameters TS: 0.4; TL: 40) for metallic silver were used.
Lorenz to Gauss rate 0 :100 and symmetric line shape for other
peaks were used. All fitting procedures are made using the
Gaussian–Lorentzian sum function. The results of surface
composition of thin silver films deposited onto PET were
compared with the ‘‘bulk’’ silver surface analysis results.
Surface cleaning with Ar+ions (3 keV, 18 AA/cm2) was used
to remove adsorbed impurities. The argon-ion cleaning was
applied to all samples.
3. Results and discussion
After 60 s exposure oxygen plasma contact angle for PET
substrate was reduced from 72- to 10- respectively, illustrating
the improvement of wettability of polymers that is a result of
the increase of its surface polar groups [11]. Oxygen plasma
like chemical etching, corona discharge plasma treatment,
irradiation by gamma ray, ultraviolet light and electrons beams
appears to be efficient treatment way of polymers. Such kind of
Table 1
The crystallite size and microstrain of Ag films on PET (as deposited and annealed at 140 -C for 30 min)
Ag cubic (111) 20 nm of Ag on PET 50 nm of Ag on PET 100 nm of Ag on PET
As-deposited Annealed As-deposited Annealed As-deposited Annealed
Crystallite size, nm 15.6 8.4 14.1 14.5 17.7 18.5
Mictrostrain, r.u. 3.54I10�3 6.64I10�3 3.92I10�3 3.84I10�3 3.14I10�3 3.00I10�3
I. Prosycevas et al. / Thin Solid Films 495 (2006) 118–123120
treatment produces relative strong adhesion of metallic film to
polymer that was demonstrated for aluminum or copper thin
films with polymers [11]. In addition [11], as the describe
observation is the same as in the case of PET ( PET: 70 -to 10-,Polysiloxan 70 - to 10 -).
3.1. XRD analysis results
XRD pattern of 20, 50 and 100 nm Ag on PET as deposited
and annealed are presented in Fig. 1. XRD peaks of Ag films
on PET substrates corresponding to (111), (200) and (311) and
(222) planes were observed. The position of these lines in XRD
patterns is similar to those observed for bulk silver [20–23].
The relative intensity of (111) peak is significantly higher than
that for Ag powder diffraction, suggesting a preferred
orientation of some Ag grains starting at very early growth
stages. According to our results the silver layers on PET of 20
nm thicknesses have strong (111) textures. This fact was also
observed for the earliest stages of the Ag (111) film on the flat
and defect-free substrate (mica) substrates [23]. Intensity of
these peaks increased with the thickness of films. The
crystallite size and microstrain of the Ag film calculated
according to [17] are presented in Table 1.
The crystallite size for the Ag films (Table 1) increased from
15.6 to 17.7 nm with increment of Ag film thickness.
According to the X-ray diffraction studies of Ag films on
PET [5] at low thickness (up to 10 nm) the crystallite size is
equal to the film thickness. Above a thickness of 10 nm the
Y, um
a
c
b
d
Z, nm
1.0
0.5
7.50
0.5
1.0
X, um
Y,
1.0
Y,
1.0
Y, um
Z, nm
1.0
0.5
170
0.5
1.0
X, um
Fig. 2. AFM images of Ag film on PET thickness: a) 20 nm, c) 50 nm, (a
crystallite size is still proportional to the film thickness, but the
crystallite growth is slower than the increment in the film
thickness [7]. In our case after annealing Ag films on PET at
140 -C for 30 min we didn’t observe drastical increase of the
average in-plane crystallite size (like it was observed in the
case of Ag films on crystalline silicon substrates after annealing
at <150 -C temperatures) [20].
Thermal annealing in our case resulted in an increase of
the grain size by 3–5% for the film of 50 and 100 nm
thickness, and decrease from 15.6 to 8.4 nm for the thickness
20 nm. The behavior of 50 and 100 nm Ag films on PET
wasn’t dependent on the dynamics of motion of PET
macromolecules taking place at temperature close to glassing
point. These films behave like films on a solid substrate
where the crystallite size increases and microstrain decreases
with annealing. Completely different behavior was observed
for films of 20 nm Ag thickness where the microstrain
increase up to 47% was found. At the early stage of growth
(up to 20 nm Ag films on PET) behavior of this film is
similar to Ag films on sapphire. At this thickness Ag films
are discontinuous over the sapphire surface [8] and film with
a thickness of less than 15 nm prepared by evaporation onto a
glass or quartz substrates consists of isolated metal islands
[22]. Exposition in air at ambient temperature and atmosphere
of such discontinuous films and thin film of 100 nm resulted
in formation of few tens of nanometer porous oxide [22]. In
our case hexagonal (Ag2O) was detected for the Ag-PET film
annealed at 140 -C.
um
Z, nm
0.5
220
0.5
1.0
X, um
um
Z, nm
0.5
450
0.5
1.1
X, um
s deposited), b) 20nm and d) 50 nm (annealed at 140 -C for 30 min).
Table 2
Morphology and grain size of Ag films on PET (as deposited and annealed at 140 -C for 30 min)
20 nm of Ag on PET 50 nm of Ag on PET 100 nm of Ag on PET
As-deposited Annealed As-deposited Annealed As-deposited Annealed
A (max. height), nm 14.9 22.3 22.0 62.3 18.1 41.8
Ra (average roughness), nm 1.34 1.98 2.22 7.57 1.45 2.66
Rq (rms), nm 1.72 2.57 2.84 9.46 1.90 3.77
Rsk (skewness), nm �0.10 0.31 �0.19 0.09 0.07 0.90
Rku (kurtosis), nm 3.51 3.74 3.25 3.03 4.17 7.02
I. Prosycevas et al. / Thin Solid Films 495 (2006) 118–123 121
3.2. AFM analysis results
Fig. 2 and Table 2 present the AFM images and statistical
analysis of morphology of evaporated and annealed Ag films.
The difference in microstucture and the particle shape of
discontinuous and semi-continuous Ag samples are clearly
seen. The grain height increased from 14.9 to 22.0 nm with
the increase of thickness of Ag film. (For comparison islands
of 20 Ag films on sapphire have typically vertical and lateral
dimensions in the 100–300 nm ranges 10–60 nm in
diameter [24]). 20 nm Ag films on PET are discontinuous
like it was for 20 nm Ag films on sapphire [8] and silicon
[24].
3.3. Optical properties
Fig. 3 shows the optical-density spectra of the Ag film on
PET in the wavelength range 300–800 nm. According to the
optical measurements, reflectivity of the film for 100 nm was
close to 10% and optical density was measured for the films
of lower thickness only. The reflectivity of 50 nm Ag film on
PET was found to increase with increasing the wavelength
from 500 to 800 nm. In these spectra, the peak around 400
nm [13] that is attributed to the surface plasmon transverse
resonance wasn’t observed. For the low thickness film (i.e. 20
nm) the absorption peak due to the surface plasmon of
longitudinal resonance of electric field vector along the length
axis [13] was found at around 750 nm wavelengths. The
400 500 600 700 800
0.2
0.4
0.6
0.8
1.0
1.2
1.4
surface plasmon
a)b)c)d)
λ, nm
Opt
ical
den
sity
(a.
u)
Fig. 3. Optical density of Ag films on PET versus wavelength (before and after
annealing) a) 20 nm, c) 50 nm, (as deposited), b) 20nm and d) 50 nm (annealed
at 140 -C for 30 min).
thermal annealing induced red shift of this peak to the higher
wavelength. According to Gan’s theory [25], the longitudinal
plasmon position shift to longer wavelength is attributed the
increase of aspect ratio (length/diameter) of the metal
nanorods formed in polymer matrix. After annealing the
intensity of this peak decreased, that could be explained as
variation of silver particles density.
3.4. Surface composition
The results of surface chemical analysis of Ag films on PET
are presented in Table 3 and Fig. 4. There are two peaks (Fig.
4) located at the same binding energy of 386.0 and 374.0 eV,
which correspond to a doublet Ag3d5/2 and Ag3d3/2 [26–28].
The Ag 3d position was stable, during thermal annealing and
surface cleaning. The presence of small Ag–O peak after
thermal annealing in air suggests that the film within the XPS
sampling depth is not fully oxidized.
100 nm silver films exhibit the same behavior during
processing of the samples— after annealing (or ageing) process
relative amount of carbon increases while amount of oxygen is
almost changeless. The relative amount of carbon after short
Ar+ion sputtering decreases sharply. On the other hand, different
picture appears for 20 nm silver film sample. The relative
amount of oxygen drops sharply after sputtering process, while
amount of carbon shows almost no changes. The peak with the
binding energy off 531.5 eV is seen in spectra for all samples. To
compare this value with X.–Y. Gao [28] results one can suggest
that this peak originates from the mixture of atomic oxygen and
hydroxyl groups. It can be found that the surface concentration
of O is very high, which could be attributed to the chemosorption
process. The significant C1s peak, which indicates to high
surface concentration of C, usually results from the adventitious
Table 3
Surface atomic concentration of Ag films on PET (d=20 and 100 nm,
Tanneal=140 -C)
Ag3d5/2 (%) O1s (%) C1s (%)
Ag 20 nm 25 26 50
Ag 20 nm on PET after annealing
at 140 -C12 33 54
Ag 20 nm on PET after annealing
at 140 -C after Ar+sputtering
44 7 49
Ag100 nm 29 22 49
Ag 100 nm on PET after annealing
at 140 -C
21 23 56
Ag 100 nm on PET after annealing
at 140 -C after Ar+sputtering
56 17 27
10000
12000
14000
16000
18000
20000
22000
280282284286288290292294
Binding Energy, eV
Inte
nsity
, a.u
.O=C-O
C-C, C-H
Fig. 5. XPS C1s spectra for 20 nm Ag film on PET annealed at 140 -C: dashed
line with crosses – acquired data.
I. Prosycevas et al. / Thin Solid Films 495 (2006) 118–123122
contaminant from the atmosphere and from the PET substrate.
On the basis of the binding energy data [27,28] fitting was for
done Ag 3d5/2. In this we suggested the presence of silver oxide
and surface plasmons. It is difficult to determine the oxidation
states of Ag because the peaks are rather close i.e. 368–368.2 for
Ag- [25,27] and 367.4 for AgO [27,29] and 367.8 for Ag2O
[27,28]. In [22] it was also observed the surface plasmon loss
peak (+3.78 eV) of silver around the interface between the silver
and dielectric layer. Fitted Ag 3d spectra (Fig. 4) for annealed at
140 -C 20 nm silver film on PET show high intensity peak at
368.2 eV and low intensity peak at 367.7 eV. Therefore we
assigned high intensity peak to metallic silver and low intensity
peak to Ag – O bounds. Relative peak area for metallic silver
and Ag – O bounds in this case is 75.9% and 24.1% respectively.
Relative peak area of metallic silver and Ag – O bounds for 100
nm oxidized silver peak is 86% and 12.5%. The Ar+ ion
sputtering of the sample surface removes oxides completely
from all samples.
AnalyzingtheC1speak(Fig.4)ofAgonPETonecanconclude
that it contains three well-separated peaks corresponding to
carbon atoms bound to carbon and hydrogen in benzene ring
(284.6 eV) and to ester carbon atoms (288.75 eV). Methylene
carbons singly bound to oxygen peak (286.3 eV) is observed in
O1s (533.8 eV), respectively. It is known [29] that in C 1s
spectra of pure PET surface the rate between C–C, C–H and
O=C–O relative peak area is 80% and 20% respectively. For
100 nm of Ag on PET C–C, C–H and O=C–O relative peak
area is 97% and 3%, for 20 nm it 89% and 10%, respectively.
The C1s peaks fitting results of all samples show the
unchangeable behavior of C1s bound for 20 nm silver films
on PET (even after annealing and sputtering) (Fig. 5). The
relative area of O=C–O bound is more higher then twice
compared to other samples (50, 100 nm). The appearance of
15000
35000
55000
75000
95000
115000
135000
364366368370372374376378Binding Energy, eV
Inte
nsity
, a.u
Ag 3d5/2
Ag 3d3/2
Ag - O
Ag
sat.
Fig. 4. Fitted XPS Ag 3d spectra for 20 nm Ag film on PET annealed at 140
-C,: crosses— acquired data, dashed line —fitted data, thin line— metallic
silver, thick line— silver bounded to oxygen, ‘‘sat.’’— satellite signal due to
nonmonochromatized Al Ka radiation.
intense O=C–O peak is clear evidence of discontinuous of thin
metal film [30].
4. Concluding remarks
Ag thin film structure, morphology and optical and surface
analysis results suggest that Ag film deposited on PET at
elevated temperatures are (111) textured, and depending on the
thickness are discontinuous (20 nm) or continuous (50–100 nm)
films. The preferred orientation of some Ag grains starts at very
early growth stages (i.e 20 nm). Formation of Ag nanorods in
PET matrix was indicated by surface plasmon longitudinal
resonance peak in UV-VIS spectra and typical peak on the XPS
spectra. Thermal annealing of these discontinuous films at
temperatures close to the glassing temperatures brings to the red
shift of plasmon resonance wavelength. Formation of discon-
tinuous structure was observed for 50 nm of Ag film on the PET
substrate, i.e. the reflectivity of this film increased with
increasing the wavelength from 500 to 800 nm. The continuous
Ag films (100 nm) presented close to 100% reflectivity. Some
kind of similarity between ‘‘bulk’’ silver and 100 nm Ag film on
PET samples surface composition can be noticed. The silver
oxidation product as hexagonal silver (I) oxide (Ag2O) was
detected on 100 nm silver layer surface after 140oC annealing.
Acknowledgements
The Lithuanian Science and Study Foundation has sup-
ported this work and is greatly acknowledged.
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