A

pBm

wg

fi

o©

K

1

p[yifil

fsimd

(

0d

Progress in Organic Coatings 60 (2007) 105–111

Effect of low-pressure O2 and Ar plasma treatments on the wettabilityand morphology of biaxial-oriented polypropylene (BOPP) film

S.M. Mirabedini a,∗, H. Arabi a, A. Salem a, S. Asiaban b

a Iran Polymer and Petrochemical Institute, P.O. Box 14965-115, Tehran, Iranb Petrochemical Company of Iran, Research and Technology, Customer Oriented Department, Iran

Received 3 December 2006; received in revised form 7 July 2007; accepted 9 July 2007

bstract

Low-pressure plasma treatments in an rf discharge of O2 and Ar were employed to introduce polar functional groups onto the biaxial-orientedolypropylene (BOPP) surfaces to enhance the wettability and activation. The effects of plasma treatment on the morphology and wettability of theOPP films were characterized using static contact angle measurements, attenuated total reflection (ATR)–FTIR spectroscopy, scanning electronicroscopy (SEM) and atomic force microscopy (AFM).A clear increase in the surface energy of BOPP films due to O2 and Ar plasma treatments was observed. The surfaces became highly hydrophilic

hen exposed for 20 s or longer to the plasma discharge. The wettability of polymer surface can be improved when oxygen functionalities areenerated, which can be achieved directly in O-containing plasmas or via post plasma reactions.

Small reduction in surface energy of plasma treated BOPP films, after 30 days aging showed that the plasma-induced cross-linking in BOPP

lm was not the dominant phenomena. With increasing the treatment power and time, rate of the decrease in surface energy after aging is reduced.AFM and SEM images revealed distinct changes in the topography of BOPP due to O2 and Ar plasma treatments. Nodular structure is formed

n the BOPP film during the treatment and the size of the nodules increases with the treatment time.2007 Published by Elsevier B.V.

gy

bast[

mftiip

eywords: BOPP; Plasma treatment; Surface energy; Wettability and morpholo

. Introduction

Polyolefins are being increasingly used for industrial pur-oses, due to their valuable properties and ability to be recycled1,2]. Biaxial-oriented polypropylene (BOPP) film in recentears has become one of the most popular, high growth filmsn the world market. BOPP film is available in a wide range oflm variations targeting the packaging, pressure sensitive tape,

abel, stationery, metallizing and decorative markets.However, the poor bondability as a result of low sur-

ace energy of such kind of materials, has limited the widepread use of these materials [3]. Thus, a further surface mod-

fication is required to attain the desired properties, while

aintaining the characteristics of the polymer bulk [4]. Tra-itionally, a variety of surface modification techniques have

∗ Corresponding author. Tel.: +98 21 4458 0040; fax: +98 21 4458 0023.E-mail addresses: m.mirabedini@ippi.ac.ir, amir mirl@yahoo.com

S.M. Mirabedini).

rrPistas

300-9440/$ – see front matter © 2007 Published by Elsevier B.V.oi:10.1016/j.porgcoat.2007.07.007

een proposed and many of them are regularly employed onn industrial scale [3,5–8]. Some of the most important of theseurface modification techniques include chemical etching, flamereatment, corona discharge, vacuum and low-pressure plasma5–9].

Cold plasma surface treatment is a powerful method used toodify surface characteristics of polymeric thin films. There-

ore, it represents an efficient, clean and economic alternativeo activate polymeric surfaces [10]. Plasma is an ionized gasncluding both charged and neutral particles, such as electrons,ons, atoms, molecules and radicals. Depending on the gas com-osition and treatment conditions, ions, electrons, fast neutrals,adicals and UV radiation contribute to the polymer treatment,esulting in etching, activation and/or cross-linking [11,12].lasma exposure of polymer surfaces causes not only a mod-

fication during the treatment, but also leaves active sites at the

urfaces, which are subject to post-reactions with coating’s func-ional groups. Plasma modification, being limited to depth offew microns, induces physical and chemical changes on the

urface without affecting the bulk.

1 n Organic Coatings 60 (2007) 105–111

tfin

2

2

wc

2

awf

•••••

otfo01

2

cswsu

Table 1Surface free energy values of probe

Liquid Surface free energy (mJ/m2)

γDlv γP

lv γ lv

Water 21.8 51.0 72.8Formamide 39.5 18.7 58.2DB

uusTor

2

Bde(

2

tsuawr

mRm

TC

T

113

1

06 S.M. Mirabedini et al. / Progress i

In this paper the effect of low-pressure O2 and Ar plasmareatments on the surface free energy and morphology of BOPPlm surfaces after modification studied using different tech-iques.

. Experimental

.1. Materials

PP 521L homopolymer film grade (BOPP), 40 �m thickness,as supplied by Sabic Petrochemical Company. O2 and Ar gas

ontainers were purchased from local suppliers.

.2. Low-pressure plasma treatment

BOPP specimens were cut into small pieces of 5 cm × 10 cmnd degreased with acetone using a soft brush. Plasma treatmentsere carried out in a K 1050X Plasma Asher Model apparatus

rom EMITECH company, with following characterizations:

Flow gauges: 15 ml/min;vacuum: 6 × 10−1 mbar;gas pressure: 0.35 bar;power output: 0–100 W;max. rf at 13.56 MHz

The degreased BOPP samples were located at the middlef the chamber using a glass support. Before the treatments,he chamber was evacuated to a pressure of about 0.6 mbar andollowed by introducing O2 into the chamber with the flow ratef 15 ml/min. The treatment was performed at a pressure of.35 bar. Each BOPP sample was treated at 10, 30 and 50 W for0, 20, 30, 60, 120, 180 and 300 s, respectively.

.3. Surface free energy calculation

Wettability of the treated specimens was evaluated as staticontact angles using a “KRUSS” G2/G40 contact angle mea-

uring system. The procedure used to measure the contact angleas based on the ASTM D 724 standard. In order to determine

urface energy of the treated BOPP samples, selected test liq-ids (analytical grade), with different values of γ l; depending

o[

A

able 2ontact angle (◦) of different probe liquid on O2 plasma treated BOPP films

ime (s) 10 W 30 W

1 2 3 4 1 2

0 98.3 86.8 57.9 50.2 98.3 86.10 87.9 71.1 57.5 38.6 85.1 71.20 77.2 68.9 56.6 27.9 73.8 68.30 70.9 49.0 53.3 20.9 68.5 55.60 69.5 48.6 56.3 20.9 67.1 53.20 67.4 46.5 56.9 21.4 65.1 50.80 58.8 45.3 58.6 20.4 60.6 49.00 49.4 45.1 58.6 20.8 48.8 45.

, water; 2, formamide; 3, diodomethene; 4, benzyl alcohol.a Due to increasing temperature, BOPP film wrinkled through the O2 plasma expos

iodomethene 50.8 0.0 50.8enzyl alcohol 29.0 9.9 38.9

pon the dispersion and polar interactions of the liquids, weretilized. The liquids were chosen to cover the broadest possiblepectrum from highly polar and disperse component; as listed inable 1. Five droplets of each liquid were tested on the surfacef each material in order to ensure the statistical validity of theesults. The measurement was completed after about 60 s.

.4. Surface analysis by FTIR–ATR technique

FTIR–ATR spectra of treated substrates were recorded on arucker IFS FTIR spectrophotometer with measurement con-itions as follows: a horizontally mounted internal reflectionlement (IRE) (germanium crystal); angle of incidence on IRE45◦); eight co-added scans; and spectral resolution of 4 cm−1.

.5. Surface morphology

A Cambridge S 360, UK, SEM was used to examine theopography of the treated BOPP specimens. In this analysis, theamples, measuring 10 mm × 10 mm, were placed in the vac-um chamber of the instrument. Samples were fixed on to anluminium stud using a double-sided cello-tape. The samplesere examined at various magnifications and the images were

ecorded photographically.The surface topography was also examined by atomic force

icroscopy (AFM) imaging with Solver-Pro SPM (NT-MDT,ussia). AFM is the one of the effective tools to examine theicrostructures of the surfaces. It is able to scan materials with-

ut any special preparation at normal temperature and pressure13].

Only tapping mode operating in height mode was applied.ll AFM images were recorded in ambient atmosphere with a

50 W

3 4 1 2 3 4

8 57.9 50.2 98.3 86.8 57.9 50.21 57.5 36.8 70.5 53.1 48.1 17.99 56.4 27.1 75.4 56.1 47.4 20.95 51.3 22.8 53.2 42.1 45.2 21.24 49.4 19.1 57.7 45.6 45.1 17.20 52.4 20.7 44.0 45.3 46.5 18.35 50.1 19.2 34.4 45.1 46.0 17.46 47.3 20.2 a

ure.

Organic Coatings 60 (2007) 105–111 107

tw

3

3

tpttfdtAtim

eoewgtbg(

γ

mbr

γ

fata

Fig. 1. Variation of surface free energy of BOPP via O2 plasma exposure time,(P: polar component, D: dispersion and T: sum of polar and dispersion compo-nents).

Fp

sfmotws

TC

T

113

1

S.M. Mirabedini et al. / Progress in

ypical relative humidity of 50%. The images consist of 500 linesith 500 points per line collected at a scan rate of 10 �m/s.

. Results and discussion

.1. Surface free energy calculation

Effects of plasma exposure time and power level on the con-act angle of different probe test liquids on BOPP samples areresented in Tables 2 and 3, respectively. The O2 and Ar plasmareatments for a relatively short time (180 s, 50 W) decreasedhe contact angle of water droplets from approximately 99◦or untreated BOPP films to less than 40◦. The contact angleecreased gradually with increasing treatment time and reachedhe lowest value (at the treatment duration time of 180–300 s).n increase of power causes a decrease of contact angle and

hus an improvement in wettability. This is probably due to thencrease of plasma ionization degree that involves an enhance-

ent of the charged species.Several methods are available for calculation of the surface

nergy of a solid [14], the particular method adopted dependsn the surface to be examined and the selected test liquids. Tostimate BOPP solid surface energy the Owens–Wendt methodas used; this method is based on a linear approximation of theeneral Fowkes expression using contact angle values of at leastwo different liquids. A more elaborate method was proposedy Schultz [15], where the surface free energy,γ; is expressedenerally as the sum of two terms, dispersion (γD) and a polarγP) component, i.e.:

= γD + γP (1)

The non-dispersive contribution (deriving from electrostatic,etallic, hydrogen bonding and dipole–dipole interactions) can

e defined as the geometric mean of polar contributions. Theesults can be shown in the following equation [15]:

lv(1 + cos θ) = 2√

γPS γP

l + 2√

γDS γD

l (2)

Thus, the dispersive γD and polar γP components of surface

S Sree energy of the substrate can be calculated from the interceptnd the slope of the expression (2). Effects of plasma exposureime and power level on the surface free energy of BOPP samplesre illustrated in Figs. 1 and 2, respectively. The figures show the

fhr

able 3ontact angle (◦) of different probe liquid on Ar plasma treated BOPP films

ime (s) 10 W 30 W

1 2 3 4 1 2

0 98.3 86.8 57.9 50.2 98.3 86.810 79.2 70.3 56.3 38.6 78.7 70.220 67.3 63.5 56.3 24.4 72.4 64.930 70.8 59.1 55.3 22.9 63.4 57.360 68.9 57.1 54.3 23.7 59.0 56.920 65.8 52.4 53.2 23.1 55.4 51.380 56.6 50.2 52.8 21.8 53.9 50.500 43.6 47.1 53.2 23.1 42.8 48.8

, water; 2, formamide; 3, diodomethene; 4, benzyl alcohol.

ig. 2. Variation of surface free energy of BOPP via Ar plasma exposure time, (P:olar component, D: dispersion and T: sum of polar and dispersion components).

urface energies of O2 and Ar plasma treated BOPP specimensor 10, 30 and 50 W power levels with the variation of treat-ent time from 10 to 300 s. The changes in the surface energy

f BOPP film significantly increased already after a very shortreatment time (20 s). Surface energy is a characteristic factorhich affects the surface properties and interfacial interactions

uch as adsorption, wetting and adhesion [16].

It is clear from figures that the polar component of the sur-

ace energy of BOPP film is significantly increased and becomesydrophilic by the plasma treatments. The polar component isesponsible for the increase of the total surface energy. Disper-

50 W

3 4 1 2 3 4

57.9 50.2 98.3 86.8 57.9 50.255.5 36.8 70.5 53.1 48.1 17.955.3 25.3 75.4 56.1 47.4 20.953.3 21.4 63.2 42.1 45.2 21.251.2 17.0 57.7 45.6 45.1 17.250.9 18.2 54.0 45.3 46.5 18.348.2 21.3 40.4 45.1 46.2 17.448.3 19.0 38.2 43.8 45.3 15.0

108 S.M. Mirabedini et al. / Progress in Organic Coatings 60 (2007) 105–111

Table 4Surface energy of BOPP film treated in gaseous plasma before and after aging

Treatment time (s) 10 W 30 W 50 W

O2 Ar O2 Ar O2 Ar

Before After Before After Before After Before After Before After Before After

30 41.1 35.2 41.7 36.2 40.3 35.3 44.2 37.1 42.9 35.2 42.1 35.660 39.9 36.3 42.3 37.1 43.3 37.3 42.6 36.8 43.5 37.2 43.6 36.7

120 38.9 35.9 43.7 37.9 43.8 38.1 39.4 37.3 44.4 36.3 40.4 36.21 37.9 45.4 38.1 48.8 43.5 48.8 39.53 37.2 45.8 38.6 a 43.7 37.8

exposure.

sttbtbi

wm[

3

tttstiiiecmf

ftegaeegrie

3

a

Ft

iatsots

catively.

Oxygen being reactive in nature, contributes mainly toincorporating groups such as OH, O C and C O O. This

80 40.5 35.5 40.2 37.1 44.500 43.6 38.9 40.7 37.2 43.8

a Due to increasing temperature, BOPP film wrinkled through the O2 plasma

ion components are almost constant prior to and after plasmareatment. The increase in surface energy [17,18] is an indica-ion of the increase in adhesion force through the relationshipetween surface energy and work of adhesion [18]. It is evidenthat if the surface free energy of a polymeric substrate is raisedy treatment to a higher level, then adhesion properties can bemproved.

The surface modifications with O2 plasma proceeds onlyith hydrophilic modification. The surface energy reached theaximum value for a short treatment time and then levels off

19].

.2. Aging effect

Treated BOPP films were aged for 30 days and then subjectedo the contact angle measurement. Values of surface energy prioro and after aging are given in Table 4. After aging, BOPP filmreated in O2 plasma, with power of 10 W, shows a decrease inurface energy by 5.9 and 4.7 mN/m for 30 and 180 s, respec-ively. These results indicate That the long exposure time maynduce cross-linking in BOPP film [19]. However, low decreas-ng in surface energy, after aging indicates that the cross-linkingnduced in BOPP film by plasma treatment was not that muchffective. This is because the BOPP films have already a highross-linking density. Because of high cross-link density, chainsobility and hence reorientation are difficult and therefore sur-

ace energy variation after aging is less evident [19].These results reveal that the effect of aging on samples treated

or a longer time is less significant as compared to samplesreated for shorter time. It is suggested that change in surfacenergy can be explained by phenomena of orientation of mobileroup [19]. For the shorter treatment time, hydrophilic groupsre incorporated on the polymer surface, and as a result, surfacenergy shows improvement for freshly treated samples. How-ver, for the samples stored for 30 days, hydrophilic groups startsetting reoriented toward each other and also toward the inte-ior. Because of this, hydrophilic groups do not face air–liquidnterface and therefore the contact angle increases and surfacenergy decreases.

.3. FTIR–ATR spectroscopy

FTIR–ATR spectra of O2 and Ar plasma treated BOPP filmsfter 30 and 180 s, and the untreated specimen are illustrated

Ft

ig. 3. FTIR–ATR spectra of untreated (—), 30 s (· · ·) and 180 s (- · -), O2 plasmareated BOPP films.

n Figs. 3 and 4. The appearance of two peaks at 1800–1591nd 1590–1490 cm−1 in the spectra of both O2 and Ar plasmareated BOPP is an evidence of chemical changes in the BOPPurface, perhaps due to oxidation [20]. The peak in the areaf 1800–1591 cm−1 is related to the C O stretching bond andhe other peak located at 1590–1490 cm−1 concerns the C Ctretching vibration.

Two-weak peaks centered around 1720–1730 and 1640 cm−1

an be assigned to carboxylic and ester groups, and aldehydesnd ketones or even to the presence of double bonds, respec-

ig. 4. FTIR–ATR spectra of untreated (—), 30 s (· · ·) and 180 s (- · -), Ar plasmareated BOPP films.

Org

iroewi

iftpfc[

3

Oiarat

F6

s[

po(is

3

(3pit

Bs

S.M. Mirabedini et al. / Progress in

s indicated as an increase in surface energy to an equilib-ium value, for O2 plasma treatment. Also, it appears thatxygen does not produce activated species with sufficientnergy to create radicals having a long lifetime to interactithin polymeric chain, and as a result, cross-linking is not

nitiated.It should be note that plasma functionalization occurs by

nclusion of active species (oxygen containing species) in theree radicals generated during the treatment and some func-ionalization can be achieved after plasma treatment; whenlasma-treated samples are exposed to ambient atmosphere, O2rom the air can rapidly react with some free radicals and thisontributes to intensify surface functionalization phenomenon19,21,22].

.4. SEM analysis

SEM micrographs of BOPP specimens treated for 60 s with2 and Ar plasma discharge under a power of 50 W are shown

n Fig. 5. As it can be seen the plasma treated samples have

slightly dented surface (Fig. 5a and b). The SEM analysis

eveals that the surface roughness increases with exposure timend this is indicative of an etching process. The topology andhe roughness of the originally smooth surfaces of the untreated

ig. 5. SEM micrographs of O2 and Ar plasma treated BOPP films at 50 W for0 s.

solicfiasaiuTofifp

tatNtt

msdis

odHs

st

anic Coatings 60 (2007) 105–111 109

ample were significantly changed after plasma treatment23].

The size of the nodules is increased for Ar-treated sam-les plasma (Fig. 5b). Different gases exhibit unlike etch ratesf polymer surface, under nominally equal plasma conditions50 W, 60 s), where Ar gas is more powerful in imposingncreased roughness by the bombardment mechanism for BOPPurface [24].

.5. AFM analysis

Fig. 6 shows AFM topographic images for (a) the untreated,b) O2 plasma treated at 10 W for 30 s, (c) O2 plasma treated at0 W for 180 s (d), Ar plasma treated at 10 W for 30 s and (e) Arlasma treated at 30 W for 180 s, BOPP film surfaces. All thesemages are 10,000 A × 10,000 A and 25,000 A × 25,000 A, withhe corresponding z ranges given above the individual images.

The topography shown in Fig. 6(a) is typical for untreatedOPP specimen. Here, the surface appears to be relatively

mooth, showing an annular and granular structure of the naturalhape of the BOPP film. These structures were totally dispersedn the film surface. The difference between the highest and theowest peak on the line was 50 nm. This topography is dom-nated by annular protrusions with boundaries between themlearly visible. O2 plasma treatment etches the surface of BOPPlm, forming aggregates on the surface as illustrated in Fig. 6(bnd c). In the images (b), the annular features are still visible, buteems rougher. With further increase of the exposure time (180 s)nd more plasma power, the surface becomes rougher, as shownn Fig. 6(c), where the annular features previously found on thentreated sample surface, care changes to a randomly-shaped.his illustrates a large number of nano-scale depressions formedn the sample surface following plasma treatment. This modi-cation in the surface morphology is thought to result mainlyrom the bombardment of the surface by the energetic particlesresent in the plasma.

While using Ar plasma treatment, the etching effect makeshe surface of the BOPP film even rougher, as shown in Fig. 6(dnd e). The longer exposure to the plasma discharge, the rougherhe surface. It can be seen that almost all the surface is etched.odular structure is formed on the BOPP surface during the

reatment and the size of the nodules increases with the treatmentime.

Plasma discharge interacts in numerous ways with a poly-er surface. At rather severe conditions, the polymer surface is

ubject to etching effects, whereby the polymer is continuouslyegraded. While chemical etching is promoted by radicals asn O2, CF4 and SF6 discharges, physical etching occurs undertrong ion bombardment, as for example in Ar plasmas [25,26].

The wettability of polymer surfaces can be improved whenxygen functionalities are generated, which can be achievedirectly in O-containing plasmas or via post-plasma reactions.owever, the new functionalities can be lost again to the atmo-

phere, resulting in a reduced surface energy [27].Furthermore, Table 5 shows the average values of root-mean-

quared (RMS) roughness obtained from the AFM analysis ofhe recorded images together with the maximum height for dif-

110 S.M. Mirabedini et al. / Progress in Organic Coatings 60 (2007) 105–111

F for 33

fdIc

TRe

UOOAA

ig. 6. AFM images of BOPP film; (a) untreated, (b) O2 plasma treated at 10 W0 s and (e) Ar plasma treated at 30 W for 180 s.

erent exposure times for O2 and Ar plasma treatments. Fiveifferent points were measured and then the average is reported.t is seen that the RMS roughness increases with plasma pro-essing time from 36.0 A for the untreated surface to 69.1 and

able 5MS roughness (A) of the BOPP surface associated with plasma dischargexposure time

Rpv (nm) RMS roughness (A)

ntreated BOPP 33.33 36.0

2, 10 W, 30 s 44.06 47.0

2, 30 W, 180 s 56.97 69.1r, 10 W, 30 s 45.93 49.5r, 30 W, 180 s 57.93 60.8

6ra

4

eBaLaB

0 s, (c) O2 plasma treated at 30 W for 180 s, (d) Ar plasma treated at 10 W for

0.8 A after 180 s exposure to O2 and Ar discharge treatment,espectively. This phenomenon is related with the weight lossnd the etching process induced by plasma treatment [19].

. Conclusion

Exposing BOPP films to low-pressure plasma is a simple andffective way for modifying and improving the wettability. TheOPP films become highly hydrophilic when exposed, even for

very short time (e.g., 20 s), to low-pressure plasma treatment.ow reduction in surface energy of plasma treated BOPP films,fter 30 days aging, revealed that the cross-linking induced inOPP film by plasma treatment was not that much effective.

Org

Tdpmf

fhBe

A

P

R

[

[

[

[[

[

[[

[

[[

[

[

[

[[

(2006) 409–416.[26] H.H. Richter, A. Wol, in: R. Hippler, S. Pfau, M. Schmidt, K.H. Schoenbach

S.M. Mirabedini et al. / Progress in

his is because the BOPP films have already a high cross-linkingensity and changes due to very small cross-linking induced bylasma, are little. Because of high cross-linking density, chainsobility and hence re-orientation are difficult and therefore sur-

ace energy variation after aging are less evident.FTIR spectra revealed chemical reactions on the BOPP sur-

ace due to O2 and Ar plasma treatments. The AFM observationsave shown the etching effect on the surface roughness of theOPP film. AFM has been proven to be a powerful tool in thexamination of surface morphology.

cknowledgement

The authors wish to thank the financial support by Nationaletrochemical Company.

eferences

[1] A. Kinloch, Adhesion and Adhesives, Chapman and Hall, New York, 1987.[2] S. Wu, Polymer Interface and Adhesion, Marcel Decker, New York, 1982.[3] J. Schultz, M. Nardin, in: A. Pizzi, K.L. Mittal (Eds.), Handbook of Adhe-

sive Technology, Marcel Decker, New York, 1994.[4] R. Li, L. Ye, Y.W. Mai, Composites 28A (1997) 73.[5] T. Zeiler, S. Kellermann, H. Nstedt, J. Adhes. Sci. Technol. 15 (2001) 653.[6] D. Cho, K.D.H. Shin, W. Lee, D. Kim, J. Adhes. Sci. Technol. 15 (13)

(2001) 1589.

[7] S.M. Mirabedinia, H. Rahimi, Sh. Hamedifar, M. Mohseni, Int. J. Adhes.

Adhes. 24 (2004) 163–170.[8] D.M. Brewis, I. Mathieson, 143 Rapra Review Reports, 12 (2002) 1317.[9] S.E. Mallakpour, R. Hajipour, A. Zadhoush, R. Mahdavian, J. Appl. Polym.

Sci. 79 (2001) 1317.

[

anic Coatings 60 (2007) 105–111 111

10] L. Carrino, G. Moroni, W. Polini, J. Mater. Process. Technol. 121 (2002)373–382.

11] E.M. Liston, L. Martinu, M.R. Wertheimer, J. Adhes. Sci. Technol. 7 (1993)1091.

12] A.C. Fozza, J.E. Klemberg-Sapieha, M.R. Wertheimer, Plasmas Polym. 4(1999) 183.

13] Q.F. Wei, Mater. Charact. 52 (2004) 231–235.14] R. Oosting, PhD Thesis, Delft University of Technology, The Netherlands,

1995.15] J. Schultz, K. Tsutsumi, J.B. Donnett, J. Colloid Interf. Sci. 59 (1977)

277.16] E. Lugscheider, K. Bobzin, Surf. Coat. Technol. 142 (2001) 755–760.17] H.Y. Nie, M.J. Walzak, B. Berno, N.S. McIntyre, J. Appl. Surf. Sci. 145

(1999) 627.18] F. Garbassi, M. Morra, E. Occhiello, Polymer Surfaces from Physics to

Technology, John Wiley & Sons, New York, 1998.19] N.V. Bhat, D.J. Upadhyay, J. Appl. Polym. Sci. 86 (2002) 925–936.20] R. Mahlberg, H.E.M. Niemi, F. Denes, R.M. Rowell, Int. J. Adhes. Adhes.

18 (1998) 283.21] M.R. Sanchis, V. Blanes, M. Blanes, D. Garcia, R. Balart, Eur. Polym. J.

42 (2006) 1558–1568.22] S.K. Oiseth, A. Krozer, B. Kasemo, Lausmaa, J. Appl. Surf. Sci. 202 (2002)

92–103.23] M. Lehocky, H. Drnovska, B. Lapcıkova, A.M. Barros-Timmons, T.

Trindade, M. Zembala, L. Lapcık Jr., Colloids Surf. A: Physicochem. Eng.Aspects 222 (2003) 125–131.

24] R.W. Paynter, Surf. Interf. Anal. 33 (2002) 14.25] O.J. Kwon, S.W. Myung, C.S. Lee, H.S. Choi, J. Colloid Interf. Sci. 295

(Eds.), Low Temperature Plasma Physics, Wiley-VCH, Berlin, 2001, p.433.

27] R.M. France, R.D. Short, Langmuir 14 (1998) 4827.

本文献由“学霸图书馆-文献云下载”收集自网络，仅供学习交流使用。

学霸图书馆（www.xuebalib.com）是一个“整合众多图书馆数据库资源，

提供一站式文献检索和下载服务”的24 小时在线不限IP

图书馆。

图书馆致力于便利、促进学习与科研，提供最强文献下载服务。

图书馆导航：

图书馆首页 文献云下载 图书馆入口 外文数据库大全 疑难文献辅助工具