Advances in Materials Science and Engineering

Advances in Materials Science and Engineering / 2008 / Article

Research Article | Open Access

Volume 2008 |Article ID 518354 |

Katsuyoshi Kondoh, Junji Fujita, Junko Umeda, Tadashi Serikawa, "Estimation of Compositions of Zr-Cu Binary Sputtered Film and Its Characterization", Advances in Materials Science and Engineering, vol. 2008, Article ID 518354, 5 pages, 2008.

Estimation of Compositions of Zr-Cu Binary Sputtered Film and Its Characterization

Academic Editor: Yiu-Wing Mai
Received28 Aug 2008
Accepted26 Nov 2008
Published14 Jan 2009


Zr-Cu amorphous films were prepared by radio-frequency (RF) magnetron sputtering on glass substrate using two kinds of the elemental composite targets: Cu chips on Zr plate and Zr chips on Cu plate. It was easy to precisely control chemical compositions of sputtered films by selecting the chip metal and the number of chips. It is possible to accurately estimate the film compositions by using the sputtered area and the deposition rate of Cu and Zr. XRD analysis on every as-sputtered film showed the broadened pattern. Zr-rich composition film, however, revealed a small peak at the diffraction angle of , and Cu-rich one indicated it at . TEM and electron diffraction analysis on the former also showed the main Zr ring patterns and its streaks. Zr-rich composition film with Cu content of 34 at% or less indicated a good corrosion resistance by salt spray test. On the other hand, Cu-rich version with 74 at% Cu or more was poor in corrosion resistance. This was because Zr was reactively passive, and caused the spontaneous formation of a hard non-reactive surface film that inhibited further corrosion than Cu.

1. Introduction

A sputtering process is useful to form the amorphous-structured films to be widely used as high-performance materials such as oxide and metallic films in the industrial fields [13]. Characteristics of the films strongly depend on their compositions and structures controlled by both sputtering conditions and compositions of target materials [46]. In particular, Zr-Cu alloys are well known as metallic glass materials [7, 8], having an obvious glass-liquid transition temperature (Tg), high strength and toughness. Bulk metallic glass (BMG) shows a high corrosion resistance due to the absence of grain boundaries [9]. Thus, a metallic glass film is a promising candidate for suitable surface treatments to improve the corrosion resistance of poor resistance light metals, such as aluminum, titanium, and magnesium alloys [1012]. In this study, RF magnetron sputtering process was applied to form Zr-Cu amorphous films with various compositions because of its advantages of the low-temperature deposition and high controllability in the deposition [13, 14]. The compositions of sputtered films were estimated by using the deposition rate and sputtered area of each metal in the composite target. The structure of the films was analyzed by XRD, and the crystallization behavior in annealing was evaluated by XRD and TEM observation. The corrosion resistance of Zr-Cu thin films was also investigated in the conventional salt spray test.

2. Experimental

Zr-Cu binary films were deposited by a 13.56 MHz radio-frequency (RF) planer-magnetron sputtering. The elementally composed targets of Zr and Cu chips and plates were used in this study. For example, a composite target having 4 pieces Cu chips on Zr disk plate was shown in Figure 1. Films were deposited on glass substrates placed on the water-cooled substrate holder in the sputtering chamber evacuated to  Pa pressure. A high-purity (99.999%) argon gas was used as a sputtering gas in 10 1.33 Pa. The chemical compositions of sputtered films were controlled by changing the number of chips. Before starting the film deposition, the presputtering was carried out by placing a shutter-plate between the target and substrate to remove the contaminated surface layer of the target. Sputtering power and sputtering gas pressure were fixed at 150 watts and 1.33 Pa, respectively. The thickness of the films was about 1 μm by 900 seconds sputtering. The annealing condition was 723 K for 900 seconds in Ar gas atmosphere. X-ray Diffraction (XRD) analysis with K- and transmission electron microscope (TEM) measurements were carried out on each sputtered film to investigate the crystallization behavior by annealing. The salt spray test (SST) according to Japan Industrial Standard (JIS) Z 2731 [15] was carried out for 96 hours to evaluate the corrosion resistance.

3. Results and Discussion

Zr-Cu amorphous thin films with various compositions are deposited by changing the number of Zr or Cu chips on another metal plate. Figure 2(a) shows XRD patterns of the sputtered films, and Cu content for each one was quantitatively measured by electron probe micro-analysis (EPMA). Basically, each shows a broadened pattern meaning an amorphous structure, that is, Zr-Cu binary sputtered films are completely amorphous in the wide range of Cu compositions. In the case of the Cu content with 34 at% or less, however, such Zr-rich films indicate a small peak at , corresponding to a crystallized zirconium as mentioned below. The Cu-rich films with 84 at% Cu or more clearly reveal a diffraction peak at . After annealing each film at 723 K for 900 seconds in Ag gas atmosphere, as shown in Figure 2(b), XRD patterns in Zr or Cu rich composition films reveal remarkably crystalline Zr and Cu peaks at and , respectively. Zr peak intensity gradually increases with increase in Zr content of the film. Figure 3(a) shows TEM observation of as-sputtered Zr-Cu film with 34 at% Cu and its electron diffraction pattern. It basically consists of an amorphous structure. Some spots, however, indicating a crystalline Zr, are detected in electron diffraction pattern. It corresponds to a small Zr peak at in Figure 2(a). As shown in Figure 3(b), the Zr-Cu sputtered film with 34 at% Cu annealed at 723 K in Ar gas consists of fine Zr crystal grains with 20 ~ 40 nm. Accordingly, two kinds of small peaks at and of as-sputtered films in Figure 2(a) correspond to the nucleation sites of crystalline Zr and Cu, respectively. They are completely crystallized by annealing at elevated temperature.

The estimation of Zr-Cu film compositions was carried out when changing the number of each chip, and compared to those measured by EPMA. In this study, it is supposed that there is no effect of the contacts between Zr and Cu atoms on each deposition rate in sputtering when employing the elemental composite Zr-Cu target. That is, the composition of Zr-Cu films is determined by both the deposition rate and the sputtered area in using the single-metal target. The EPMA result indicates that Cu composition ratio of each sputtered film is in proportional to the number of chips when using both of Zr and Cu chips. That is, it is possible to control the sputtered film composition by selecting the metal chip and its number of pieces. Concerning the estimation of the film compositions by using the deposition rate, for example, Cu content of the film () is simply expressed by the sputtered area and deposition rate as shown in (1) where is a deposition rate and S is sputtered area.

When considering that the density of the sputtered film is constant, the following equation is obtained where t; film thickness (μm), M; atomic mass, y; amount of substance per unit area (mol).

In (2), y value of each metal corresponds to each deposition rate (), and estimated by measuring the film thickness (t) in using each metal target. In this experiment,  mol and  mol are obtained when the thickness of the Cu film and Zr one are 0.8335 μm and 2.1767 μm, respectively. Then, the ration of each deposition rate () is 5.081. Furthermore, by using this value, Cu content of the film is calculated by the following (3):

Figure 4 indicates a relationship between Cu composition ratio by EPMA and Cu sputtered area ratio (β). When using the composite targets which consist of Zr chips and Cu plate, EPMA measurement corresponds to the calculated values with .

The previous study reported that was 3.9 ~ 4.0 when using argon ion sputtering with a reflection ion energy of 100 ~ 300 eV. Accordingly, the estimation of the film compositions by (3) is significantly accurate. On the other hand, in the case of the target consisting of Cu chips and Zr plate, the measured Cu content is smaller than that of calculated values with . This is because of the gradual decrease of Cu intensity () with increase in the sputtering time as shown in Figure 5. The brown color of as-received Cu chip surface changed into dark brown after discharging in 2.4 kiloseconds. The Cu intensity, however, shows a stably constant value () in using Zr chips on the Cu plate. EPMA on the dark brown Cu chip specimen indicated that Zr fine particles originated in the target plate covered the chip surface, and caused the reduction of Cu deposition rate in sputtering.

Figure 6 shows the salt spray test results of as-sputtered films with various Cu contents on the silica glass plate. The specimens with Cu content of 34 at% or less indicates a good corrosion resistance even after continuously spraying for 96 hours. The conventional 316 stainless steel, which is one of the standard corrosion resistant materials, also shows no damage after 96 hours SST under the same conditions. In the case of 56 at% Cu content, the sputtered film reveals locally damaged area around the glass plate. It means the corrosion is due to the poor bonding between the film and glass plate. The Zr-rich films with crystallized Zr peaks annealed at 723 K also show no corrosion damage after SST for 96 hours. In considering the standard electrode potential of Zr (−1.539 V) and Cu (+0.337 V), the voltage (1.876 V) is effective to accelerate the galvanic corrosion in the crystallized film. However, as mentioned above, this film showed no corrosion damage. It is well known that Zr easily forms passive films in heating under oxidizing atmosphere [16]. In the SST on the crystallized Zr-rich film after annealing, the passivation due to zirconium oxides causes the control of the corrosion phenomenon. On the other hand, with increase in Cu content of the sputtered films, the poor passivation of Cu is not effective to obstruct corrosion damages in SST as shown in Figure 6.

4. Conclusion

The accurate estimation of the sputtered film compositions was carried out by calculating the deposition rate in sputtering and the sputtered area of each metal used in the composite target. In the case of Cu chips on Zr plate target, the measured Cu contents of the film was smaller than the calculated values because of the reduction of Cu deposition rate due to Zr fine particles covering the Cu chip surface. All as-sputtered films showed a broadened pattern in XRD analysis. After annealing at 723 K, Zr-rich composition film indicated a small peak of crystallized Zr at . Zr-rich films with 34 at% Cu or less had a good corrosion resistance in SST, and their annealed ones including Zr crystals also showed excellent properties because of the passivation of crystallized zirconium in the film.


  1. Y.-M. Sung and D.-W. Han, “Transparent conductive titanium-doped indium oxide films prepared by a magnetic null discharge sputter source,” Vacuum, vol. 83, no. 1, pp. 161–165, 2008. View at: Publisher Site | Google Scholar
  2. K. Fujiwara, H. Tanimoto, and H. Mizubayashi, “Elasticity study of very thin Cu films,” Materials Science and Engineering A, vol. 442, no. 1-2, pp. 336–341, 2006. View at: Publisher Site | Google Scholar
  3. A. Ishida and M. Sato, “Ti-Ni-Cu shape-memory alloy thin film formed on polyimide substrate,” Thin Solid Films, vol. 516, no. 21, pp. 7836–7839, 2008. View at: Publisher Site | Google Scholar
  4. B. Marsen, E. L. Miller, D. Paluselli, and R. E. Rocheleau, “Progress in sputtered tungsten trioxide for photoelectrode applications,” International Journal of Hydrogen Energy, vol. 32, no. 15, pp. 3110–3115, 2007. View at: Publisher Site | Google Scholar
  5. V. Sittinger, A. Pflug, W. Werner et al., “Production of MF and DC-pulse sputtered anti-reflective/anti-static optical interference coatings using a large area in-line coater,” Thin Solid Films, vol. 502, no. 1-2, pp. 175–180, 2006. View at: Publisher Site | Google Scholar
  6. C. Fu, C. Yang, L. Han, and H. Chen, “The thickness uniformity of films deposited by magnetron sputtering with rotation and revolution,” Surface and Coatings Technology, vol. 200, no. 12-13, pp. 3687–3689, 2006. View at: Publisher Site | Google Scholar
  7. T. Nagase and Y. Umakoshi, “Effect of electron irradiation on nano-crystallization in Zr66.7Cu33.3 and Zr65.0Al7.5Cu27.5 amorphous alloys,” Materials Science and Engineering A, vol. 343, no. 1-2, pp. 13–21, 2003. View at: Publisher Site | Google Scholar
  8. Y. K. Kuo, K. M. Sivakumar, C. A. Su et al., “Measurement of low-temperature transport properties of Cu-based Cu-Zr-Ti bulk metallic glass,” Physical Review B, vol. 74, no. 1, Article ID 014208, 7 pages, 2006. View at: Publisher Site | Google Scholar
  9. V. Schroeder, C. J. Gilbert, and R. O. Ritchie, “Comparison of the corrosion behavior of a bulk amorphous metal, Zr41.2Ti13.8Cu12.5Ni10Be22.5, with its crystallized form,” Scripta Materialia, vol. 38, no. 10, pp. 1481–1485, 1998. View at: Publisher Site | Google Scholar
  10. X. Liu, G. S. Frankel, B. Zoofan, and S. I. Rokhlin, “In-situ observation of intergranular stress corrosion cracking in AA2024-T3 under constant load conditions,” Corrosion Science, vol. 49, no. 1, pp. 139–148, 2007. View at: Publisher Site | Google Scholar
  11. K. H. W. Seah, R. Thampuran, X. Chen, and S. H. Teoh, “Comparison between the corrosion behaviour of sintered and unsintered porous titanium,” Corrosion Science, vol. 37, no. 9, pp. 1333–1340, 1995. View at: Publisher Site | Google Scholar
  12. H. Huo, Y. Li, and F. Wang, “Corrosion of AZ91D magnesium alloy with a chemical conversion coating and electroless nickel layer,” Corrosion Science, vol. 46, no. 6, pp. 1467–1477, 2004. View at: Publisher Site | Google Scholar
  13. V. S. Veerasamy, H. A. Luten, R. H. Petrmichl, and S. V. Thomsen, “Diamond-like amorphous carbon coatings for large areas of glass,” Thin Solid Films, vol. 442, no. 1-2, pp. 1–10, 2003. View at: Publisher Site | Google Scholar
  14. P. J. Fallon, V. S. Veerasamy, C. A. Davis et al., “Properties of filtered-ion-beam-deposited diamondlike carbon as a function of ion energy,” Physical Review B, vol. 48, no. 7, pp. 4777–4782, 1993. View at: Publisher Site | Google Scholar
  15. Japan Industrial Standard (JIS),
  16. P. R. Roberge, Corrosion Engineering: Principles and Practice, McGraw-Hill, New York, NY, USA, 2008.

Copyright © 2008 Katsuyoshi Kondoh et al. This is an open access article distributed under the Creative Commons Attribution License, which permits unrestricted use, distribution, and reproduction in any medium, provided the original work is properly cited.

More related articles

 PDF Download Citation Citation
 Download other formatsMore
 Order printed copiesOrder

Related articles