Journal of Metallurgy

Journal of Metallurgy / 2014 / Article

Research Article | Open Access

Volume 2014 |Article ID 346328 |

Shimaa H. El-Hadad, Khaled M. Ibrahim, Lothar Wagner, "Characteristics of Anodized Layer in Investment Cast Ni50Ti50 Shape Memory Alloy", Journal of Metallurgy, vol. 2014, Article ID 346328, 6 pages, 2014.

Characteristics of Anodized Layer in Investment Cast Ni50Ti50 Shape Memory Alloy

Academic Editor: Michael E. Kassner
Received27 Dec 2013
Accepted06 Jan 2014
Published25 Feb 2014


NiTi shape memory alloys are promising implant materials due to their shape memory effect and super elasticity. In the current study, some Ni50Ti50 (mass %) SMAs samples were prepared by investment casting. These samples were then anodized and thermally treated to improve the surface properties. A fully saturated oxide layer was obtained. The structure and hardness properties of the anodized surfaces were then investigated. A hard porous layer with no free Ni atoms could be obtained which can be used as prebiomimetic surface for biological application.

1. Introduction

NiTi shape memory alloys (SMAs) are promising materials to develop state-of-the-art devices in the medical and dental field. The pseudoelasticity and shape memory effect of these alloys give them unique properties over the wide range of the developed alloys [1, 2]. In addition, NiTi possesses high corrosion resistance by virtue of a titanium oxide film naturally formed over its surface. Owing to these desirable thermomechanical properties and chemical stability, NiTi is becoming a popular biomaterial [3, 4]. However, the high nickel content has hampered the wider applications of these materials. Excessive surface corrosion and wear of NiTi raise health concerns because Ni ions released to body tissues and fluids can induce toxic and allergic responses [5]. By choosing a suitable surface modification method [6], hardness and corrosion resistance as well as biocompatibility of NiTi shape memory alloy can be improved. Among these methods, those not involving a high temperature during treatment (preferably less than 300°C) are particularly important because NiTi is very sensitive to heat treatment. Exposure of NiTi to a high temperature treatment may disrupt or remove the prescribed built-in properties [7].

Anodization is a common and simple low-temperature process employed for thickening the oxide film over the surface of Ti and its alloys. Sharma [8] showed unexpected differences between anodization of NiTi alloys and Ti alloys [9]. In order to further investigate anodization of Ni-Ti alloy, surface anodization was applied in the current work. Characteristics, hardness, and corrosion of the thin film obtained by anodization were investigated.

2. Experimental

2.1. Samples Preparation

Ni-Ti alloy samples were prepared by using an investment casting technique. A double vacuum melting process was performed to ensure the quality, purity, and properties of the material. Ingots of Ni50Ti50 (mass %) were melted in a vacuum induction skull melting (ISM) furnace. The molten metal was then poured in a ceramic mold. Two cast bars with 30 mm diameter and 300 mm length were obtained and then machined to (25 mm × 250 mm) bars. The samples were wire cut and then studied by using optical (OM) and scanning electron microscopies (SEM).

2.2. Anodization

Samples of 5 mm thickness were wire cut from the as-cast bars for the anodization purpose. The samples were then polished with SiC papers of different grades and finally with 0.1 μ alumina paste. The polished samples were cleaned in acetone and then in deionized water before anodization. Anodization was carried out in a cell consisting of NiTi as the anode and stainless steel 316L as cathode. A solution of [1 M H2SO4  + 0.15 wt% HF] was used as electrolyte and kept at room temperature. The NiTi samples were anodized at 10 V for 1 h and then cleaned in deionized water. Some selected samples were chosen for carrying out hydrothermal treatment in water at 170°C for 18 h. The surface morphology of the anodized and bare samples was studied using SEM. The surface compositions of the samples were acquired using X-ray diffraction of the NiTi thin film (TF-XRD) before and after anodization and thermal treatments.

2.3. Hardness Testing

The indentation method was usually adopted to test the hardness because of its unique simplicity and economy. A Vickers micro-hardness tester (cone) was employed to measure the hardness values of the deposited film at a normal load of 0.49 N.

2.4. Corrosion Testing

The corrosion test was carried out in order to know the corrosion resistance of the sample before and after anodization. This test was done in three electrode cells. Potentiodynamic polarisation experiments were carried out in Hank’s solution, whose composition is given in Table 1. A pH of 7.4 and normal human body temperature of 37°C were maintained throughout the experiment. The procedures were conducted in accordance with ASTM standard G5–94 using PGSTAT30 potentiostat. The specimen, with an area of 1 cm2, was exposed to the Hank’s solution for 5 min prior to potentiodynamic polarisation. A stable open circuit potential (OCP) was monitored. Saturated calomel electrode (SCE) was used as reference electrode. The recorded potentiodynamic polarization curves were used to obtain the characteristic parameters for corrosion behaviour, that is, corrosion current density () pitting potential () and corrosion rate. These parameters were typically determined by extrapolation of the Tafel lines of each polarization curve. The as-corroded surface of the samples was investigated using SEM and the corrosion products were also analyzed using energy dispersive spectroscopy (EDX).

NaCl8 g/L
KCl0.4 g/L
NaHCO30.35 g/L
KH2PO40.06 g/L
Na2HPO40.0475 g/L
C6H12O6 (glucose)1 g/L

37°C: Hank's physiological solution buffered with HEPES (3.5745 g/L) at the normal physiological pH of 7.4.

3. Results and Discussion

3.1. Microstructure and Characteristics of the Anodized Film

The microstructure of the sample (as-cast Ni50:Ti50) is shown in Figure 1. According to Ni:Ti phase diagram, Figure 2, the microstructure is composed of the matrix corresponding to the intermetallic phase TiNi, and it contains few particles frequently present in the sample which is Ti2Ni. After anodization, the surface microstructure was changed to semiporous structure. The surface microstructure of the as-anodized samples and the corresponding cross section are shown in Figures 3(a) and 3(b). The as-anodized samples obtained a white color, which didn’t change apparently after subsequent hydrothermal treatment. According to Karambakhsh et al. [10], the color saturation of the anodized layer (chromaticity) in sulfuric acid solution reaches its maximum value (white color) when the applied voltage is equal to 10 v. In the current case, the solution is different but the same color was obtained due to the similar used voltage. A well-defined anodized layer containing semiporous structure, Figure 3(a), with approximately 1 μ size was obtained in this sample. This porous structure is typical for fixation of bone implants [11].

The cross section of the anodized sample showing the thin film obtained by anodization is presented in Figure 3(c). It is clear that an anodized layer in order of 2 μ was obtained. In this micrograph, some cracks (denoted by white arrow) can be seen in the formed film. This can be attributed to the formation of pathways for oxygen evolution during anodization or shrinkage of the anodization products during dry-up in air after removal from the electrolyte [12, 13].

3.2. Hydrothermal Treatment of the Anodized-As-Cast Sample

In order to reveal the oxide layer, the hydrothermal treatment was performed for the as-cast sample after being anodized. Figures 4(a)4(d) present the surface topography and magnified micrographs of the anodized sample after treatment and the corresponding XRD pattern. Comparing the surface morphology presented in Figures 4(a)4(d) to that of as-anodized sample before treatment shown in Figure 3(a), obvious differences in the nature of the anodized layer can be observed. The pores relatively increased in size and some of them formed smaller pores inside, as denoted by white arrows Figure 4(c). This could be attributed to the excessive corrosion of TiO2 during the hydrothermal treatment. Moreover, a new white phase appeared on the pore edges, represented by white arrows in Figure 4(b).

The XRD patterns of the anodization products on the samples after 18 h of hydrothermal treatment are, respectively, shown in Figure 4(d). Before hydrothermal treatment, the XRD pattern showed only one prominent peak between angles 20° and 60°. This peak and all the other diffraction lines were assigned to NiTi substrate itself. The prominent 110 peak in the presented pattern belongs to the austenite phase. However, the anodized layer was visually observed as white color representing the maximum saturation of the anodized layer as discussed earlier. This means the deposited film is amorphous which is in agreement with previous pieces of work [14, 15].

After hydrothermal treatment, NiTi2 phase occurred at an angle of 42.28°. Since this phase was absent in the pattern of the untreated samples, thus it follows the detected NiTi2 phase that is present in the modified surface of the treated samples rather than in the substrate. This phase is the white phase denoted by arrow in Figure 4(b). However, we still couldn’t observe TiO2 because we still have amorphous structure.

The formation of TiO2 tubes and changing their diameter are a complex process that involves physical, chemical, electrochemical, and many other factors. Xue et al. [16] divided this process into four stages: (1) formation of a dense barrier oxide layer under the strong electric field (Ti + 2H2O → TiO2 + 4H+), (2) chemical dissolution of TiO2 to form cylindrical pores due to F-ions from electrolyte (TiO2 + 4H+ + 6F → Ti + 2H2O), (3) dissolution of the porous layer resulting in final tube structure with extension of oxidation time, and (4) excessive corrosion of TiO2 tubes to form wires. These variables, voltage, duration, pH, and ion concentration, are four types of forcing functions for the formation of wires and tubes in the anodization process. Therefore, measuring these parameters and their effectiveness on the anodized structure is suggested for future work.

Concluding, the above process can be mainly ascribed to the dissolution of Ti leading to decreasing pH value and then F-that plays an important role in the dissolution of TiO2 layer. So the formation of wires or tubes is affected not only by voltage and duration but also by pH and ion concentration.

3.3. Characteristics of the Anodized Layer after Isothermal Holding

In the previous section, the hydrothermal treatment showed some influence on the nature of anodized layer. However, the TiO2 couldn’t be clearly detected by XRD which means that most of the layer is still in its amorphous state. Therefore, the samples were further heated at 2°C/min to 450°C and then hold for 3 hours followed by furnace cooling. The XRD of isothermally treated samples is shown in Figure 5. The tetragonal Rutile TiO2 could be obtained along with hexagonal Ni3Ti phase. This indicates the transformation of the anodized layer from the amorphous to crystalline structure after the hydrothermal treatment.

It was reported by Tian et al. [17] that Ni3Ti layer forms due to Ni atoms diffusion from the free surface and their accumulation in the region with the lowest oxidation state that is close to metal-oxide interface. Since Ni3Ti appears as a line phase in the Ni-Ti phase diagram, the amount of Ni in the intermetallic Ni3Ti layer becomes saturated upon formation of this layer. If more Ni content was present, Ni metallic particles may be formed. The absence of free Ni in the XRD pattern is a good indication of the success of the anodized layer to suppress Ni release to the surface. This result implies that by controlling the thickness and the oxidation state of the oxide layer, Ni release can be feasibly prevented.

3.4. Anodization and Surface Hardness

Since hardness is an essential property to consider in biomaterials applications, we found that it is necessary to evaluate hardness after surface anodization and compare it to the bare NiTi area of the as-cast sample. The hardness of the anodized thin film shown in Figure 3(c) was measured as 500 HV while that of the bare NiTi was 200 HV. This means, the hardness of the as-cast sample was more than the double due to anodization. It is concluded that the deposition of gradient films could effectively improve the surface hardness of the current NiTi samples.

3.5. Corrosion Behavior of Cast Ni50Ti50 Alloy

The as-cast samples were corrosion tested in a Hank’s biological solution. Figures 6(a) and 6(b) show the SEM micrograph and the corresponding EDS analysis of the sample after corrosion testing. The corrosion products were found frequently and were characterized by the presence of Na and Cl. The electrochemical properties were obtained from the polarization curve. The electrochemical properties obtained from the Tafel curve were , OCP, corrosion rate of  A cm−2, −182 mV, and mm/year, respectively. Corrosion testing of the as-anodized sample showed an excellent resistance to corrosion, thus the Tafel curves appeared as vertical lines. This means that the corrosion resistance of NiTi in Hank’s solution has been improved by the anodizing introduced in this study.

4. Conclusions

In the current study, characteristics of anodized layer in Ni50Ti50 shape memory alloy were investigated and the following observations were concluded:(i)the oxide film observed after isothermal holding was characterized by the absence of free Ni atoms/particles which is a typical requirement in terms of biocompatibility;(ii)the anodized layer exhibited increased surface hardness and excellent corrosion resistance in contrast to untreated samples. This is also an advantage when this alloy is used as biomaterial for some specific implant which requires higher hardness and excellent corrosion resistance in the body fluid.

Conflict of Interests

The authors declare that there is no conflict of interests regarding the publication of this paper.


The authors would like to thank the laboratory of corrosion and surface protection at Central Metallurgical Research and Development Institute, Egypt for performing the anodization treatments.


  1. N. K. Simha, “Fundamental theories and mechanisms of failure,” in Comprehensive Structural Integrity, I. Milne, R. O. Ritchie, and B. Karihaloo, Eds., vol. 2, pp. 573–606, Elsevier Science, 2003. View at: Google Scholar
  2. Y. Zheng, L. Cui, and J. Schrooten, “Temperature memory effect of a nickel-titanium shape memory alloy,” Applied Physics Letters, vol. 84, no. 1, pp. 31–34, 2004. View at: Publisher Site | Google Scholar
  3. N. Bayat, S. Sanjabi, and Z. H. Barber, “Improvement of corrosion resistance of NiTi sputtered thin films by anodization,” Applied Surface Science, vol. 257, no. 20, pp. 8493–8499, 2011. View at: Publisher Site | Google Scholar
  4. F. T. Cheng, P. Shi, G. K. H. Pang, M. H. Wong, and H. C. Man, “Microstructural characterization of oxide film formed on NiTi by anodization in acetic acid,” Journal of Alloys and Compounds, vol. 438, no. 1-2, pp. 238–242, 2007. View at: Publisher Site | Google Scholar
  5. K. K. Das, S. N. Das, and S. A. Dhundasi, “Nickel, its adverse health effects & oxidative stress,” Indian Journal of Medical Research, vol. 128, no. 4, pp. 412–425, 2008. View at: Google Scholar
  6. G. S. Firstov, R. G. Vitchev, H. Kumar, B. Blanpain, and J. Van Humbeeck, “Surface oxidation of NiTi shape memory alloy,” Biomaterials, vol. 23, no. 24, pp. 4863–4871, 2002. View at: Publisher Site | Google Scholar
  7. N. Shevchenko, M.-T. Pham, and M. F. Maitz, “Studies of surface modified NiTi alloy,” Applied Surface Science, vol. 235, no. 1-2, pp. 126–131, 2004. View at: Publisher Site | Google Scholar
  8. A. K. Sharma, “Anodizing titanium for space applications,” Thin Solid Films, vol. 208, no. 1, pp. 48–54, 1992. View at: Google Scholar
  9. H. Habazaki, M. Uozumi, H. Konno, K. Shimizu, P. Skeldon, and G. E. Thompson, “Crystallization of anodic titania on titanium and its alloys,” Corrosion Science, vol. 45, no. 9, pp. 2063–2073, 2003. View at: Publisher Site | Google Scholar
  10. A. Karambakhsh, A. Afshar, S. Ghahramani, and P. Malekinejad, “Pure commercial titanium color anodizing and corrosion resistance,” Journal of Materials Engineering and Performance, vol. 20, no. 9, pp. 1690–1696, 2011. View at: Publisher Site | Google Scholar
  11. S. J. Simske and R. Sachdeva, “Cranial bone apposition and ingrowth in a porous nickel-titanium implant,” Journal of Biomedical Materials Research, vol. 29, no. 4, pp. 527–533, 1995. View at: Publisher Site | Google Scholar
  12. J. Ryhänen, E. Niemi, W. Serlo et al., “Biocompatibility of nickel-titanium shape memory metal and its corrosion behavior in human cell cultures,” Journal of Biomedical Materials Research, vol. 35, pp. 451–457, 1997. View at: Google Scholar
  13. J. Kawakita, M. Stratmann, and A. W. Hassel, “High voltage pulse anodization of a NiTi shape memory alloy,” Journal of the Electrochemical Society, vol. 154, no. 6, pp. C294–C298, 2007. View at: Publisher Site | Google Scholar
  14. M. H. Wong, F. T. Cheng, and H. C. Man, “Comparison of corrosion resistance and apatite-forming ability of NiTi treated by different low-temperature methods,” Journal of Alloys and Compounds, vol. 466, no. 1-2, pp. L5–L10, 2008. View at: Publisher Site | Google Scholar
  15. A. Balyanov, J. Kutnyakova, N. A. Amirkhanova et al., “Corrosion resistance of ultra fine-grained Ti,” Scripta Materialia, vol. 51, no. 3, pp. 225–229, 2004. View at: Publisher Site | Google Scholar
  16. C. Xue, F. Zhang, S. Chen, Y. Yin, and C. Lin, “Tailoring the surface morphology of TiO2 nanotube arrays connected with nanowires by anodization,” Materials Science in Semiconductor Processing, vol. 14, no. 2, pp. 157–163, 2011. View at: Publisher Site | Google Scholar
  17. H. Tian, D. Schryvers, D. Liu, Q. Jiang, and J. Van Humbeeck, “Stability of Ni in nitinol oxide surfaces,” Acta Biomaterialia, vol. 7, no. 2, pp. 892–899, 2011. View at: Publisher Site | Google Scholar

Copyright © 2014 Shimaa H. El-Hadad 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

1055 Views | 488 Downloads | 4 Citations
 PDF Download Citation Citation
 Download other formatsMore
 Order printed copiesOrder

Related articles

We are committed to sharing findings related to COVID-19 as quickly as possible. We will be providing unlimited waivers of publication charges for accepted research articles as well as case reports and case series related to COVID-19. Review articles are excluded from this waiver policy. Sign up here as a reviewer to help fast-track new submissions.