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Materials Research

Print version ISSN 1516-1439On-line version ISSN 1980-5373

Mat. Res. vol.6 no.1 São Carlos Jan./Feb. 2003

http://dx.doi.org/10.1590/S1516-14392003000100005 

DLC-Si protective coatings for polycarbonates

 

 

J.C. DamascenoI; S.S. Camargo Jr.I; M. CremonaII

IEngenharia Metalúrgica e de Materiais, Universidade Federal do Rio de Janeiro, C.P. 68505, 21945-970 Rio de Janeiro, RJ, Brazil
IIDepartamento de Física, Pontifícia Universidade Católica do Rio de Janeiro, C.P. 38071, 22454-970 Rio de Janeiro, RJ, Brazil

Address to correspondence

 

 


ABSTRACT

In this work, a-C:H:Si (DLC-Si) films were produced onto crystalline silicon and polycarbonate substrates by the rf-PACVD technique from gaseous mixtures of CH4 + SiH4 and C2H2 + SiH4. The effects of self-bias and gas composition upon mechanical and optical properties of the films were investigated. Micro-hardness, residual stress, surface roughness and refractive index measurements were employed for characterization. By incorporating low concentrations of silicon and by exploring the more favorable conditions for the rf-PACVD deposition technique, highly adherent DLC-Si thin films were produced with reduced internal stresses (lower than 1 GPa), high hardness (around 20 GPa) and high deposition rates (up to 10 µm/h). Results that show the technological viability of this material for application as protective coatings for polycarbonates are also discussed.

Keywords: thin films, DLC, chemical vapor deposition, silicon carbide, polycarbonate


 

 

1. Introduction

Plastics have become important materials because they can be produced in large scale and are cheaper and lighter than many other materials. Amongst those, polycarbonates are well-known, commercially available materials. Because of their excellent breakage resistance, polycarbonates have replaced glasses in many applications, such as automobile headlamps, safety shields of windows, ophthalmic lenses and sunglasses, and the like. However, their use is still limited to non-abrasive and chemical-free environments, because of their low hardness, low scratch resistance and their high susceptibility to harsh chemical conditions. To overcome this limitation, methods for producing a hard transparent protective coating on polycarbonate materials have been studied1-5, including the deposition of diamond-like amorphous carbon (DLC) films6-9.

DLC films have been successfully deposited on different kinds of substrates by several different techniques10,11. Their high hardness, low friction coefficient and high chemical inertness have made of them great candidates for wear-resistant, hard coatings for many applications. Unfortunately, the high intrinsic stress of these films limits their adhesion and thickness. Silicon-incorporated diamond-like carbon films (DLC-Si) have a great potential for solving some of the major drawbacks of pure DLC films. Indeed, DLC-Si films present reduced residual internal stress12,13, high deposition rates14, good adhesion to most substrates, including various metal alloys, steels and glasses15-17 and very high hardness16,18,19.

In this work, DLC-Si films were produced onto crystalline silicon and polycarbonate substrates by the rf-PACVD technique from gaseous mixtures of CH4 + SiH4 and C2H2 + SiH4 . The effects of self-bias and gas composition upon mechanical and optical properties of the films were investigated.

 

2. Experimental

Silicon-incorporated hydrogenated amorphous carbon films (DLC-Si) were deposited from gaseous mixtures of CH4 + SiH4 and C2H2 + SiH4 onto crystalline silicon and polycarbonate substrates placed on the cathode of a conventional radio frequency (13.56 MHz) parallel plate glow discharge reactor. A gas flow of about 10 sccm from pre-made mixtures with 5 vol.% of silane was fed into the reactor through mass flow controllers. During all deposition runs the electrode distance and the chamber pressure monitored by a capacitance manometer were kept fixed at 3 cm and 2.0 Pa, respectively. Films with thickness between 1.5 and 3 mm were produced at different self-bias voltages (VB) from -100 V up to -1000 V. It must be noted that no temperature control of the substrate was done during deposition. Therefore, substantial heating of the substrate surface may occur as a result of its interaction with the plasma, mainly in case of depositions with high power densities.

Residual internal stress was obtained by the substrate bending method using a Dektak IIA stylus profilometer, which was also used for the thickness and surface roughness measurements. All films presented compressive stresses. Indentation of the samples was done with a Vickers diamond micro-indenter with a 0.25 N load during approximately 20 s keeping the indentation depth smaller than 20% of the sample thickness. Hardness was obtained from the measurement of the indentation diagonals on an optical microscope using the DIC (differential interference contrast) technique. In all cases hardness was calculated from the average of a series of 20 different indentations. All stress and hardness measurements were taken from samples deposited on silicon substrates, while roughness was determined for the films deposited on polycarbonate.

Refractive index was measured by the Abelés-Hacskaylo20 method using a 633 nm He-Ne laser beam. All optical measurements were made using the samples deposited on polycarbonate substrates.

 

3. Results and Discussion

Deposition rate of DLC-Si films is strongly increased when one increases the rf power density dissipated in the plasma in a similar manner to what is observed for pure a-C:H films. As can be seen in Fig. 1, the deposition rate as a function of the resulting cathode self-bias potential presents an increase of almost one order of magnitude when the self-bias voltage is varied from -100 V to -1000 V. In addition, the deposition rate obtained when using C2H2 as carbon-source gas is much higher than in case of CH4. For instance, films deposited with CH4 present a maximum deposition rate of about 2.7 mm/h whereas with C2H2 a deposition rate of 10 mm/h was achieved keeping the other deposition conditions unchanged. Similar behavior was also observed for pure a-C:H films21 and can be explained considering the following: (a) the low ionization energies of C2H2 in comparison to CH4 which allows the first to react in higher quantities with the growing film surface; and (b) the increased C/H-ratio for C2H2 (1:1) compared with CH4 (1:4).

 

 

Figures 2a and 2b show the behavior of surface roughness of polycarbonate samples, before and after deposition of the films, as a function of cathode self-bias and gas precursor. As one can see in these figures, the surface roughness of the polycarbonate samples is slightly raised by the plasma deposition process for |VB| up to 600 V, maintaining acceptable low surface roughness regardless of the source gases used. On the other hand, samples deposited with values of |VB| of 800 V are greatly damaged by the plasma having their surface roughness raised by almost two orders of magnitude for both gas mixtures. The surface damage of the samples can be attributed to high-energy particle bombardment when using high power densities, which can lead to substantial surface heating and fusion. For this reason, polycarbonate substrates were not used for deposition at VB = -1000 V.

Residual internal stress of DLC-Si films strongly depends on the employed cathode self-bias potential, as already reported elsewhere22. In the low self-bias range the internal stress is increased when one increases the self-bias voltage, attains a maximum and then decreases monotonically for high values of self-bias, as shown in Fig. 3a. It is interesting to observe that this maximum value occurs around VB = -200 V for CH4-based films and around V= 400 V for C2H2-based films. Similar behavior was also observed for pure a-C:H films21. This can be explained by considering that on impact at the surface, ions from a CnHm gas plasma fragment into n separate C+ ions, evenly distributing among then the incident energy. Since the material densification and, consequently, the residual stress generated in the films depends directly on this energy, the point of maximum stress is shifted to higher negative self-bias values when the gas precursor is changed from CH4 to C2H2 because the number of carbon atoms per molecule is also increased23. In addition, residual stress values for C2H2-based films were found to be higher than CH4-based ones.

Figure 3b shows the obtained behavior of hardness for the two series of films as a function of the cathode self-bias. As one can notice in both cases a monotonic increase of hardness is observed when the self-bias is varied from 100 V up to -400 V. For |VB| > 400 V, the hardness of CH4based films is decresead very slightly, while in case of C2H2based films, higher values of hardness were obtained. Indeed, in contrast to what is generally observed for DLC films21, 24 a significant reduction of hardness for high values of negative self-bias was not observed in agreement with our previous results22.

Measurements of refractive index of the films were carried out as a function of cathode self-bias and gas precursor. As can be observed in fig. 4, in case of CH4-based films there is an increase of the refractive index from 1.71 to 1.90 when the self-bias is varied from -100 V to -400 V, and a slightly reduction to 1.86 for VB = -600 V. The refractive index of C2H2-based films is increased monotonically from 1.81 to 1.90 when one varies the self-bias from -100 V to -600 V. Optical measurements for VB = -800 V and -1000 V could not be obtained due to the surface damage of the samples as discussed before. Obtained values of refractive index of all films are higher than the refractive index of the polycarbonate substrate (n = 1.586). Therefore, although these films can be good candidates for the use as protective coatings for polycarbonate, they cannot be used as anti-reflective coatings. This issue will be further investigated by varying the source gas mixture composition.

 

 

4. Conclusions

The viability of producing DLC-Si films deposited by PECVD as protective coatings for polycarbonate substrates has been demonstrated. A study of the influence of deposition parameters, namely self-bias and gas composition, on the properties of the films was carried out. Films deposited at high self-bias showed very high deposition rates, low stress and high hardness. However, high self-bias values leaded to surface damage of the samples. Smooth films could be obtained keeping self-bias voltages below |VB| = 600 V so that to avoid surface heating and damage. Acetylene seems to be more attractive as carbon source gas since much higher deposition rates can be obtained while other properties like surface roughness, refractive index and hardness are equivalent to films deposited from methane mixtures.

 

Acknowledgements

This work was supported by Finep and CNPq Brazilian agencies, CNPq/DLR International Cooperation Program and DLR/BMBF (Germany).

 

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Address to correspondence:
S.S. Camargo Jr.
e-mail:
camargo@metalmat.ufrj.br

Received: January 02, 2002
Revised: September 30, 2002

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