Synthesis of High Coercivity Core–Shell Nanorods Based on Nickel and Cobalt and Their Magnetic Properties
© to the authors 2009
Received: 25 July 2009
Accepted: 2 October 2009
Published: 21 October 2009
Hybrid magnetic nanostructures with high coercivity have immense application potential in various fields. Nickel (Ni) electrodeposited inside Cobalt (Co) nanotubes (a new system named Ni @ Co nanorods) were fabricated using a two-step potentiostatic electrodeposition method. Ni @ Co nanorods were crystalline, and they have an average diameter of 150 nm and length of ~15 μm. The X-ray diffraction studies revealed the existence of two separate phases corresponding to Ni and Co. Ni @ Co nanorods exhibited a very high longitudinal coercivity. The general mobility-assisted growth mechanism proposed for the growth of one-dimensional nanostructures inside nano porous alumina during potentiostatic electrodeposition is found to be valid in this case too.
KeywordsMagnetic nanowires Nanorods Hybrid nanostructures Core–shell nanostructures Mobility-assisted growth mechanism
Nanostructured materials such as nanowires, nanotubes and nanorods are drawing considerable attention of the scientific community because of their tremendous application potential in various fields such as solar cells, field sensors, bioseparation and medical therapy . Designing and controlling the morphology and growth of these nanowire and nanotubes will surely impact the development of nanotechnology [2, 3]. The landmark paper on carbon nanotubes by Iijima  led to a surge in research activities in the area of organic and inorganic one-dimensional nanostructures . Inorganic one-dimensional nanostructures like nanotubes and nanowires assume significance because of their diverse utilities in sensor technology, high density magnetic storage, delivery vehicles, catalysis and selective separation [5, 6]. Various methods are in vogue for the synthesis of metal nanotubes and nanowires. These include various wet-chemical routes [5, 7–9] and physical techniques such as electrochemical deposition, pulse laser deposition and molecular beam epitaxy [10–12].
Metallic magnetic nanotubes/wires of Ni, Co and Fe and also their alloys such as FePt, CoPt, NiFe, NiZn, CoCu and FeB were investigated in great detail due to their application potential in diverse fields such as perpendicular recording, cell separation, diagnosis, therapeutics and magnetic resonance imaging [2, 13–18]. Most of these structures are based on pore wall modification or wet-chemical methods . Magnetic nanostructures synthesized via the earlier-mentioned routes are often impure and rendered useless for applications . Template-assisted technique is an elegant technique for fabricating one-dimensional structures, and most of the reported template-assisted methods are based on the chemical modification of porous templates such as etched polymer membrane or anodized alumina (AAO). Template-assisted electrodeposition is a simple, low-cost and unique method for the preparation of one-dimensional structures with very high purity and control .
Controlled synthesis of smart nanostructures based on magnetic materials assumes important due to their potential applications in various fields and the possibility for manipulating these structures using an external magnetic field [19, 20]. Earlier, the authors reported the synthesis of Nickel nanowires (Ni NWs), Cobalt nanowires (Co NWs)  and Cobalt nanotubes (Co NTs)  employing different precursors by a single step potentiostatic electrodeposition technique. A general mobility-assisted growth mechanism has been proposed for the growth of one-dimensional nanostructures during electrodeposition for the first time, and the veracity of the mobility-assisted mechanism inside porous alumina has been tested using different precursors. Recently, the authors also tested the veracity of mobility-assisted growth mechanism inside MWCNTs and could fabricate co-axial multifunctional nanostructures of MWCNTs and Co NTs .
Core–Shell nanostructures represent a novel class of hybrid materials, where composition and microstructure varies through the radial direction . The Co–Ni system is special due to the fact that the magnetic properties, especially, its coercivity can be tuned by varying the Co content . Cobalt is known for its contribution in modifying the magnetic properties because of its high uniaxial anisotropy. However, this is more true in the bulk and the magnetic interactions taking place at the interface at Ni @ Co could be entirely different, where they are in the nano regime. Several groups attempted to synthesize various magnetic alloys using template-assisted electrodeposition [14–17], and they achieved this by mixing the electrolyte precursors in different compositional ratios. The lacuna of such techniques is the unpredictability in the magnetic properties such as coercivity of the resultant one-dimensional structures after electrodeposition. Co-axial hybrid magnetic structures synthesized via a two-step electrodeposition technique can possibly surpass this problem by controlling the deposition of one of the components. It was shown earlier that a single-step template-assisted electrodeposition method could be employed for the fabrication of one-dimensional magnetic nanostructures [2, 13]. The authors successfully fabricated various multifunctional nanostructures and concluded that a mobility-assisted mechanism is responsible for the growth of such nanostructures . Co nanotubes could be fabricated using template-assisted growth and if these structures can be employed as further template for electrodeposition, systems such as Ni @ Co could be fabricated. Such a method of preparation for hybrid magnetic nanostructures was not found to be attempted earlier. Moreover, the growth parameters can be easily optimized. This paper reports the fabrication of such a one-dimensional system namely Ni @ Co nanorods, which is essentially a core–shell architecture (Ni as core and Co as shell) and studies on their structural and magnetic properties.
Results and Discussion
High crystallinity of Ni NWs is evident from the ED pattern, and the formation of face-centered cubic (fcc) Ni is also verified. Figure 2c depicts the FESEM images of Ni @ Co nanorods. Co NTs have been electrodeposited inside AAO membrane using Cobalt acetate as described earlier for 1 h, and then Ni is electrodeposited using NiSO4·6H2O also for 1 h. This has resulted into Ni-filled Co nanotubes (Ni @ Co nanorods) of length 15 μm and of diameter ~150 nm. The formation of a core–shell nanostructure with Co NT as shell and Ni NW as core is abundantly clear from the TEM image (Fig. 2d). It is to be noted that from the TEM image, some portion of the Co NTs remain unfilled. It can also be seen from the top portion of the FESEM image (Fig. 2c) that Ni is not completely filled inside Co NTs. The growth of nanowires/nanotubes initiates from the bottom portion of the alumina template. The incomplete filling of Ni may be due to the difference in the growth rate between Ni and Co, as their precursors are being different. Moreover, the extra hydration layer in Ni ions also may reduce the mobility and in turn the growth rate. This has supporting evidence from the energy dispersive spectroscopy (EDS).
The Ni @ Co nanorods display a room temperature coercivity of 200 Oe. This coercivity is much higher than the bulk coercivity values of both the Ni (H c = 0.7 Oe) and Co (H c = 10 Oe) . The enhanced coercivity in Ni @ Co nanorods emanate from the enhanced shape anisotropy. Li et al. reported  a similar coercivity value for Co nanotubes synthesized via template-assisted synthesis; however, the values were smaller than our earlier reports on Co NTs of very high aspect ratio . This is due to the fact that the shape anisotropy of the samples mentioned in the earlier report is much higher (aspect ratio of Co NTs is ~330) than that of the present (aspect ratio of Ni @ Co nanorods is ~100). The coercivity value for Ni @ Co nanorods is higher than that reported for Ni NWs  possessing a higher aspect ratio, and this is due to the presence of cobalt. This indicates that one can tailor the coercivity of these heterostructures by controlling the aspect ratio as well as cobalt content. M(H) curve at 6 K exhibit an enhanced coercivity of ~380 Oe. This is much higher than the other reported values of Co-based alloy nanowires . The enhancement in coercivity at low temperatures is consistent with the monotonic increase of uniaxial anisotropy constant with decreasing temperature, with the basic assumption that the shape anisotropy is independent of temperature for high aspect ratio tubes .
Similar to Co NTs , Co NWs and Ni NWs , squareness ratio (Mr/Ms) of the Ni @ Co nanorods is small. This may be due to the very high magnetic dipolar interrod interaction. This type of hybrid magnetic system with higher aspect ratio can render very high coercivity with the higher contribution of shape anisotropy and higher coercivity hybrid nanorods can find applications in fields such as data storage where a high coercivity is required. This can be achieved by extending the electrodeposition for longer deposition times and aspect ratio up to three times (~330) that of the present value (~100), using the AAO template of 60 μm thickness.
A novel magnetic nanostructure called Ni @ Co nanorods with Ni NW as core and Co NT as shell was synthesized using a two-step electrodeposition method. Structural studies indicate the formation of Ni and Co in two phases. Magnetic studies showed that Ni @ Co nanorods exhibited high longitudinal coercivity, and they can find applications in various fields where high coercivity is required. Understanding the growth mechanism also opens possibility for tuning the magnetic properties by extending the electrodeposition for longer times to obtain very high coercivity hybrid nanowires.
TNN acknowledges the financial support received from Interconnect Focus Center at Rensselaer Polytechnic Institute, Troy, New York, USA. TNN thanks Council of Scientific and Industrial Research, India for financial support in the form of CSIR-SRF.
- Liu Z, Elbert D, Chien CL, Searson PC: Nano. Lett.. 2008, 8: 2166. COI number [1:CAS:528:DC%2BD1cXosF2gsLw%3D]; Bibcode number [2008NanoL...8.2166L] 10.1021/nl080492uView ArticleGoogle Scholar
- Narayanan TN, Shaijumon MM, Ajayan PM, Anantharaman MR: J. Phys. Chem. C. 2008, 112: 14281. COI number [1:CAS:528:DC%2BD1cXhtValurnF] 10.1021/jp8035007View ArticleGoogle Scholar
- Meng GW, Jung YJ, Cao A, Vajtaj R, Ajayan PM: PNAS. 2005, 102: 7074. COI number [1:CAS:528:DC%2BD2MXks12gu74%3D]; Bibcode number [2005PNAS..102.7074M] 10.1073/pnas.0502098102View ArticleGoogle Scholar
- Iijima S: Nature. 1991, 354: 56. COI number [1:CAS:528:DyaK38Xmt1Ojtg%3D%3D]; Bibcode number [1991Natur.354...56I] 10.1038/354056a0View ArticleGoogle Scholar
- Bao J, Tie C, Xu Z, Zhou Q, Shen D, Ma Q: Adv. Mater.. 2001, 13: 21. 10.1002/1521-4095(200111)13:21<1631::AID-ADMA1631>3.0.CO;2-RView ArticleGoogle Scholar
- Steinhart M, Wehrsphon RB, Gosele U, Wendroff JH: Angew. Chem. Int. Ed.. 2004, 43: 1334. COI number [1:CAS:528:DC%2BD2cXivFSksb4%3D] 10.1002/anie.200300614View ArticleGoogle Scholar
- Yanagishita T, Nishio K, Masuda H: Adv. Mater.. 2005, 17: 2241. COI number [1:CAS:528:DC%2BD2MXhtVKqsbvK] 10.1002/adma.200500249View ArticleGoogle Scholar
- Nielsch K, Castano FJ, Matthias S, Lee W, Ross CA: Adv. Engg. Mater.. 2005, 7: 4.Google Scholar
- Lee W, Scholz R, Nielsch K, Gosele U: Angew. Chem. Int. Ed.. 2005, 44: 6050. COI number [1:CAS:528:DC%2BD2MXhtVKqs7nE] 10.1002/anie.200501341View ArticleGoogle Scholar
- Martin CR: Science. 1991, 266: 1961. Bibcode number [1994Sci...266.1961M] Bibcode number [1994Sci...266.1961M] 10.1126/science.266.5193.1961View ArticleGoogle Scholar
- Heydon GP, Hoon SR, Farley AN, Tomlinson SL, Valera MS, Attenborough K, Schwarzacher W: J. Phys. D Appl. Phys.. 1997, 30: 1083. COI number [1:CAS:528:DyaK2sXisFGltbk%3D]; Bibcode number [1997JPhD...30.1083H] 10.1088/0022-3727/30/7/004View ArticleGoogle Scholar
- Sharif R, Shamaila S, Ma M, Yao LD, Yu RC, Han XF, Khaleeq-ur-Rahman M: Appl. Phys. Lett.. 2008, 92: 032505. Bibcode number [2008ApPhL..92c2505S] Bibcode number [2008ApPhL..92c2505S] 10.1063/1.2836272View ArticleGoogle Scholar
- Narayanan TN, Shaijumon MM, Ci L, Ajayan PM, Anantharaman MR: Nano. Res.. 2008,1(6):465. COI number [1:CAS:528:DC%2BD1MXhtFSjtr3N] 10.1007/s12274-008-8049-9View ArticleGoogle Scholar
- Li D, Thompson RS, Bergmann G, Lu JG: Adv. Mater.. 2008, 20: 1. 10.1002/adma.200890067View ArticleGoogle Scholar
- Talapatra S, Tang X, Padi M, Kim T, Vajtai R, Sastry GVC, Shima M, Deevi SC, Ajayan PM: J. Mater. Sci.. 2008, 44: 2271. Bibcode number [2008JMatS..44.2271T] Bibcode number [2008JMatS..44.2271T] 10.1007/s10853-008-3015-1View ArticleGoogle Scholar
- Li XZ, Wei XW, Ye Y: Mater. Lett.. 2009, 63: 578. COI number [1:CAS:528:DC%2BD1MXhtVKgtA%3D%3D] 10.1016/j.matlet.2008.12.002View ArticleGoogle Scholar
- Wu CU, Lin HL, Shau NL: J. Solid State Electrochem.. 2006, 10: 198. COI number [1:CAS:528:DC%2BD28XhtFSnsrk%3D] 10.1007/s10008-004-0622-xView ArticleGoogle Scholar
- Fu L, Yang J, Bi Q, Liu W: Nanoscale Res. Lett.. 2009, 4: 11. COI number [1:CAS:528:DC%2BD1MXht1Kgs70%3D]; Bibcode number [2009NRL.....4...11F] 10.1007/s11671-008-9195-4View ArticleGoogle Scholar
- Ou FS, Shaijumon MM, Ajayan PM: Nano. Lett.. 2008, 8: 1853. COI number [1:CAS:528:DC%2BD1cXmsVKhur0%3D]; Bibcode number [2008NanoL...8.1853O] 10.1021/nl080407iView ArticleGoogle Scholar
- Narayanan TN, Suchand Sandeep CS, Shaijumon MM, Ajayan PM, Philip R, Anantharaman MR: Nanotechnology. 2009, 20: 285702. COI number [1:STN:280:DC%2BD1MvjvFGksw%3D%3D] 10.1088/0957-4484/20/28/285702View ArticleGoogle Scholar
- Cao H, Wang L, Qiu Y, Wu Q, Wang G, Zhang L, Liu X: Chem. Phys. Chem.. 2006, 7: 1500. COI number [1:CAS:528:DC%2BD28Xnt1Olu7s%3D]Google Scholar
- Chikazumi S: Physics of magnetism. Wiley, New York; 1964.Google Scholar
- Henry Y, Ounadjela K, Piraux L, Dubois S, George JM: Duvail Eur. Phys. J. B. 2001, 20: 35. COI number [1:CAS:528:DC%2BD3MXktlOrsbw%3D]; Bibcode number [2001EPJB...20...35H] 10.1007/s100510170283View ArticleGoogle Scholar