# Hcp cobalt nanocrystals with high magnetic anisotropy prepared by easy one-pot synthesis

L. Meziane, C. Salzemann, Corinne Aubert, H. Gérard, C. Petit, Marc Petit

► To cite this version:

L. Meziane, C. Salzemann, Corinne Aubert, H. Gérard, C. Petit, et al., Hcp cobalt nanocrystals with high magnetic anisotropy prepared by easy one-pot synthesis. Nanoscale, 2016, 8, pp.18640-18645 10.1039/C6NR05792F. hal-01393430

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Cite this: DOI: 10.1039/c6nr05792f

Received 22nd July 2016.
Accepted 18th October 2016

DOI: 10.1039/c6nr05792f

www.rsc.org/nanoscale

# Hcp cobalt nanocrystals with high magnetic anisotropy prepared by easy one-pot synthesis†

L. Meziane,ª C. Salzemann,ª C. Aubert,ᵇ H. Gérard,ᶜ C. Petit*ª and M. Petit*ᵇ

Herein we describe the first synthesis of pure mono-disperse spherical hcp-nanocrystals ferromagnetic at room temperature. Our strategy, based on the simple combination of oleylamine and ClCo(PPh₃)₃, allows the one-pot synthesis of size-controlled hcp-nanocrystals. The size and shape of the nanocrystals can be tuned by varying the reaction time or the concentration.

Recent studies have shown that nanocrystals (NCs) can play an important role in many different fields.¹ In biology,² they can be used in a new drug-delivery system²ᵇ or in hyperthermia treatment of cancer.²ᶜ In catalysis, NCs are applied in a wide range of reactions³ with different behaviors depending on the morphology.³ª In magnetism,⁴ a wide range of applications can be found starting from the storage of information⁴ª to nano-electronics and spintronics⁴ᵈ and also magnetocaloric materials, designing new alloys allowing cooling.⁵ Among these materials cobalt NCs are of particular interest due to their unique magnetic properties. Indeed cobalt NCs exist in three crystalline forms, hcp (hexagonal close-packed), fcc (face-centered cubic) and ε-cobalt; the first one being the most interesting in terms of magnetic properties due to its high magnetocrystalline anisotropy.⁶ Indeed, the use of magnetic nanoparticles for high density storage of information requires small nanoparticles with high magneto-crystalline anisotropy at usable temperature.⁴ Moreover, several publications relate the use of cobalt NCs in catalysis. However, to use such nanocrystals for these applications, in magnetism or catalysis, it is necessary to control the shape, size, phase and purity of the surfaces. Putzer published the first synthesis of hcp-Co reporting a shape control of the NPs in 1995.⁷ The authors described

the synthesis of hcp-Co nanodisks by the decomposition of Co(OH)₂ in basic aqueous media. Under such conditions, the formation of a cobalt oxide surface was impossible to eradicate and hence this synthesis was not further used. Nowadays, polyol synthesis of nanoparticles appears to be one of the “simplest” routes to prepare NPs involving the reduction of inorganic salt at high temperature (depending on the polyol).⁸ This is also the most representative approach of a complicated mixture synthesis of nanoparticles as variations in the polyols, cobalt salt, surfactant, even bi-surfactant mixture, and ruthenium seed additive allow us to obtain different shapes, sizes and phases (mainly fcc-Co and hcp-Co) of nanocrystals (Scheme 1a).⁹ However, in the last few decades, two other processes have been developed to produce mono-disperse Co NCs under milder conditions using Co(0 or 1) organometallic precursors instead of inorganic salts (Scheme 1b). The first one is related to Carbonyl Metal Complexes (CMC) and their thermal decomposition to generate nanoparticles. For example, the thermolysis of Co₂(CO)₈ allows the formation of nanoparticles of different sizes and shapes depending on the surfactants/

<figure><img src="image_3.png" /></figure>

**Previous work** (Size and Shape depending on the mixture of reagents)

**a) Polyol approach**

<figure><img src="image_4.png" /></figure>

**b) Organometallic approaches**

<figure><img src="image_5.png" /></figure>

**This work** (Size and shape depending on concentration and reaction time)

<figure><img src="image_6.png" /><figcaption>**Scheme 1** Different approaches to cobalt nano-objects.</figcaption></figure>

<footnote>ªSorbonne Universités, UPMC Univ Paris 06, MONARIS, UMR CNRS 8233, Case 52, 4 Place Jussieu, 75252 Paris Cedex 05, France. E-mail: christophe.petit@upmc.fr</footnote>

<footnote>ᵇSorbonne Universités, UPMC Univ Paris 06, Institut Parisien de Chimie Moléculaire, UMR CNRS 8232, Case 229, 4 Place Jussieu, 75252 Paris Cedex 05, France. E-mail: marc.petit@upmc.fr</footnote>

<footnote>ᶜSorbonne Universités, UPMC Univ Paris 06, Laboratoire de Chimie Théorique, UMR CNRS 7616, 4 Place Jussieu, 75252 Paris Cedex 05, France</footnote>

<footnote>†Electronic supplementary information (ESI) available. See DOI: 10.1039/c6nr05792f</footnote>
<table><caption>**Table 1** Comparisons between cobalt(i) and cobalt(ii) complex reduction</caption><thead><tr><th>Entry</th><th>Co source</th><th>Reducing reagent</th><th><i>T</i> (°C)</th><th>Solvent</th><th>Surfactant</th><th>NPs<sup>a</sup></th></tr></thead><tbody><tr><td>1</td><td>Cl<sub>2</sub>Co(PPh<sub>3</sub>)<sub>2</sub></td><td>No</td><td>190</td><td>OAm</td><td>OAm</td><td>No</td></tr><tr><td>2</td><td>ClCo(PPh<sub>3</sub>)<sub>3</sub></td><td>No</td><td>190</td><td>OAm</td><td>OAm</td><td>MD<sup>b</sup></td></tr><tr><td>3</td><td>ClCo(PPh<sub>3</sub>)<sub>3</sub></td><td>NaBEt<sub>3</sub>H</td><td>rt</td><td>Toluene</td><td>OAm</td><td>PD<sup>c</sup></td></tr><tr><td>4</td><td>ClCo(PPh<sub>3</sub>)<sub>3</sub></td><td>NaBEt<sub>3</sub>H</td><td>rt</td><td>Toluene</td><td>OAc</td><td>PD<sup>c</sup></td></tr><tr><td>5</td><td>ClCo(PPh<sub>3</sub>)<sub>3</sub></td><td>NaBH<sub>4</sub></td><td>rt</td><td>Toluene/water</td><td>OAc</td><td>PD<sup>c</sup></td></tr><tr><td>6</td><td>Cl<sub>2</sub>Co(PPh<sub>3</sub>)<sub>2</sub></td><td>NaBH<sub>4</sub></td><td>190</td><td>OAm</td><td>OAm</td><td>No</td></tr></tbody></table>

<sup>a</sup> All synthesis were run for 1 hour. <sup>b</sup> Monodispersity (MD) was observed by TEM. <sup>c</sup> Polydispersity (PD) was observed by TEM.

ligands present in the medium adopting mainly the new ε-cobalt phase.<sup>10</sup>

It is worth noting that “to obtain a pure fraction of hcp-Co disks containing no ε-spheres, it is necessary to physically separate the two populations after the reaction is quenched” as pointed by Puntes.<sup>11</sup> The second one deals with Hydrocarbyl Complexes (HC) such as Co(η<sup>3</sup>-C<sub>8</sub>H<sub>13</sub>)(η<sup>4</sup>-C<sub>8</sub>H<sub>12</sub>) that readily decompose at lower temperature (around 150 °C) under dihydrogen pressure (usually 3 bars).<sup>12,13</sup> Depending on the presence of a polyphenylenoxide polymer or a mixture of oleic acid, oleylamine, and more recently rhodamine, spheri-cal,<sup>12</sup> nanowires<sup>13</sup> or disk-shaped<sup>14</sup> hcp-Co NCs can be respect-ively obtained. However, if these two last conditions are milder with no reduction step, the use of carbon monoxide as a ligand (CMC approach) or hydrogen pressure (HC approach) still requires specific equipment in the laboratory.

Moreover, these organometallic precursors are not readily available on a large scale and often annealing is necessary to obtain pure hcp-Co phases.<sup>15</sup>

Thus, it is still a real challenge to develop a more simple synthesis procedure for pure hcp-Co nano-objects. Based on cobalt(ii) salt and cobalt(0 or i) organometallic approaches, we decided to develop an in-between strategy. The idea is to use well-defined cobalt(i) halide complexes in the presence of oleylamine (OAm) which should act as a solvent, a surfactant and a reducing reagent (Scheme 1).<sup>16</sup>

We chose to use the cobalt(i) complex ClCo(PPh<sub>3</sub>)<sub>3</sub> which has several advantages over other organometallic precursors.<sup>17</sup> Its synthesis can be carried out on a very large scale (more than 30 grams in our laboratory), using cheap and easy to handle reagents (triphenylphosphine: TPP, sodium-boro-hydride: NaBH<sub>4</sub>). Moreover ClCo(PPh<sub>3</sub>)<sub>3</sub> is fairly stable in the solid state and can be synthesized and manipulated outside a glove-box. We first studied the synthesis of cobalt nano-particles using the method of Sun<sup>16b</sup> with the cobalt(ii) complex Cl<sub>2</sub>Co(PPh<sub>3</sub>)<sub>2</sub> (entry 1, Table 1) or with the cobalt(i) complex ClCo(PPh<sub>3</sub>)<sub>3</sub> (entry 2, Table 1) in OAm at 190 °C. The Co(ii) complex did not form any nanoparticles as already observed by Sun with Co(acac)<sub>2</sub>. However, using the analog Co(i) complex, after 1 hour we observed the formation of spherical shaped monodisperse Co-NCs as confirmed by Transmission Electron Microscopy, TEM (Fig. 1). These two first results suggest that oleylamine is a too weak reducing reagent for the cobalt(ii) salt, but enough for the cobalt(i) complex. In order to reduce the reaction temperature, we tried

<figure><img src="image_7.png" /><figcaption>**Fig. 1** 9.2 nm spherical cobalt nanoparticles with 6% polydispersity self-organized in (A) 2D and (C) thin 3D assemblies as obtained by drop deposition on amorphous carbon. (D) Superlattices obtained by slow evaporation on a graphite substrate.</figcaption></figure>

to use the complex ClCo(PPh<sub>3</sub>)<sub>3</sub> in the presence of more con-ventional reducing reagents (NaBH<sub>4</sub> or NaBEt<sub>3</sub>H) and in the presence of oleylamine (OAm) or oleic acid (OAc) (entries 3–5, Table 1). However, in all the cases the formation of only poly-morphic and polydisperse NPs was observed (see ESI Fig. S1†). It is surprising to note that NaBH<sub>4</sub> is not reducing enough for the cobalt(i) complex when the solvent is OAm and no NPs can be formed even at 190 °C (entry 6). Hence, only the protocol described in entry 2 allows the formation of 9.2 nm spherical Co NPs, characterized by very low polydispersity of 6% (Fig. 1A and B). This NP size distribution favors self-organization in a long range 2D hexagonal ordering (Fig. 1A) and thin 3D assem-blies (Fig. 1C) as obtained by simply depositing a drop of solu-tion containing NPs onto amorphous carbon substrates. When a concentrated solution is allowed to slowly evaporate on a graphite substrate, well-developed supracrystals sitting on their larger flat facets are observed (Fig. 1D). This is the charac-teristic of the formation of the so called “supracrystals” result-ing from the 3D periodic arrangement of the nanocrystals either in fcc or hcp organization.<sup>18,19</sup>

<figure><img src="image_8.png" /></figure>
<figure><img src="image_9.png" /></figure>

This is due to the attractive van der Waals interactions between the metallic core and the “chemical bonds” of self-assemblies resulting from the interdigititation of the ligand molecules.¹⁸ It should be noticed from Fig. 1A that the deduced interparticles distance is 4.1 nm, which drastically limits the interparticle interaction.²⁰ As a consequence no aggregation occurs in the solvent or on the substrates during the deposition process. Indeed the 2D patterns are purely hexagonal and also the thin 3D patterns (Fig. 1A and C). In the case of dipole-dipole interaction non-close-packed superlattices are often observed,²¹ which is not the case here (Fig. 1 and 2A). Indeed, we can affirm that no aggregation occurs in solution due to dipolar interaction.

The structural characterization has been performed by TEM and high resolution TEM (Fig. 2). A typical electronic diffraction pattern (Fig. 2B) obtained for a collection of nanocrystals (Fig. 2A) consists of 7 diffraction rings characterized by 0.216 nm, 0.203 nm, 0.190 nm, 0.146 nm, 0.125 nm, 0.114 nm and 0.106 nm distances from the center to the outward ring, respectively.

<figure><img src="image_10.png" /><figcaption>**Fig. 2** Structural characterization of cobalt NPs (A) bright field image, (B) electronic diffraction of an assembly of NPs, (C) dark field image corresponding to the (002) and (101) reflections, (D) HRTEM image and the corresponding FFT (E). Circle on (B) corresponds to the diffraction conditions for the dark field image.</figcaption></figure>

These distances correspond to the (100), (002), (101), (102), (110), (103) and (201) planes of the hcp structure of cobalt metal, when compared with the bulk values (Table 2). It must be noted that the rings are constituted of a collection of spots typical of the different nanocrystal orientations. To determine the crystallinity of the Co NCs, a dark field image (Fig. 2C) corresponding to a bright field image (Fig. 2A) were compared on a collection of particles considering the first triplet of the hcp structure (i.e. corresponding to the (100), (002) and (101) planes). NCs not oriented in the Bragg direction appear black whereas the ones in the Bragg direction appear very bright. The fact that the NCs are uniformly bright or dark gives evidence of the monocrystallinity of the particles. The HRTEM image taken on individual nanocrystals exhibits three different lattice planes (Fig. 2D). This is well illustrated in the calculated power spectra which have three reflection pairs labeled 1, 2 and 3 (Fig. 2E). The deduced distances $d_1 = 0.220$ nm and $d_2 = 0.198$ nm $\approx d_3 = 0.196$ nm correspond to the {101} and {100} reflections of the hcp structure for lattice parameters (a = 0.254 nm and c = 0.416 nm) slightly higher than for bulk values (Table 2). Both lattice plane distances and the angle between the directions $d_1, d_2$ (63.3°) and $d_2, d_3$ (52.9°) are characteristic of hcp Co NCs in the [011] orientation. Thus, both the electron diffraction of a collection of NCs and the structural investigation of an individual NC confirm the formation of monocrystalline hcp Co NCs.

Knowing the magnetic anisotropy of the hcp Co ($K = 4.1 \times 10^5$ J m$^{-3}$), the superparamagnetic diameter of a spherical NC is given by $D_{cr}^{\text{spm}} = \left(\frac{6}{\pi}V_{cr}^{\text{spm}}\right)^{1/3}$ where $D_{cr}^{\text{spm}}$ is the superparamagnetic critical diameter and $V_{cr}^{\text{spm}} \approx \left(\frac{25k_bT}{K}\right)$ is the volume of ferromagnetic particles obtained on SQUID apparatus at room temperature, $T = 300$ K.²² These estimations presume spherical particles with a very large measurement time compared to the Neel relaxation time of the magnetic nanocrystals. The case here is that SQUID measurements need about 60 s per point when the relaxation time is on a nanosecond scale.²³ For hcp cobalt NCs, the deduced critical diameter is 8 nm, i.e. particles larger than 8 nm should be ferromagnetic at

<table><caption>**Table 2** Theoretical reticular distances for bulk hcp Co, distorted hcp Co, and fcc Co compared to the experimental value. All data are in Å</caption><thead><tr><th>h</th><th>k</th><th>l</th><th>dhkl(fcc) theoretical</th><th>dhkl(hcp) theoretical</th><th>dhkl(hcp) theoretical (2% of distortion)</th><th>dhkl(hcp) experimental</th></tr></thead><tbody><tr><td>1</td><td>0</td><td>0</td><td>2.171</td><td>2.200</td><td></td><td>2.20</td></tr><tr><td>0</td><td>0</td><td>2</td><td>2.025</td><td>2.080</td><td></td><td>2.08</td></tr><tr><td>1</td><td>0</td><td>1</td><td>1.916</td><td>1.945</td><td></td><td>1.95</td></tr><tr><td>1</td><td>0</td><td>2</td><td>1.485</td><td>1.511</td><td></td><td>1.51</td></tr><tr><td>1</td><td>1</td><td>0</td><td>1.254</td><td>1.270</td><td></td><td>1.24</td></tr><tr><td>1</td><td>0</td><td>3</td><td>1.150</td><td>1.173</td><td></td><td>1.16</td></tr><tr><td>2</td><td>0</td><td>0</td><td>1.086</td><td>1.100</td><td></td><td>—</td></tr><tr><td>1</td><td>1</td><td>2</td><td>1.067</td><td>1.084</td><td></td><td>1.07</td></tr><tr><td>1</td><td>1</td><td>1</td><td>2.046</td><td></td><td></td><td></td></tr><tr><td>2</td><td>0</td><td>0</td><td>1.772</td><td></td><td></td><td></td></tr><tr><td>2</td><td>2</td><td>0</td><td>1.253</td><td></td><td></td><td></td></tr><tr><td>3</td><td>1</td><td>1</td><td>1.069</td><td></td><td></td><td></td></tr></tbody></table>
<figure><img src="image_11.png" /><figcaption>Fig. 3 (A) *M*(*H*) curve obtained for isolated 9.2 nm spherical hcp Co NCs in solution measured at 3 K (black line) and 300 K (red line). (B) Same particles in interaction (deposited on polymeric substrates).</figcaption></figure>

room temperature. This should be the case of the present
9.2 nm hcp cobalt nanocrystals. To confirm this assumption,
magnetic measurements have been performed on the isolated
nanocrystals dispersed in solution (i.e. without magnetic inter-
actions). Typical *M*(*H*) curves are reported in Fig. 3 A at 3 K
(black line) and 300 K (red line). They are normalized by the
magnetization at saturation, *M*<sub>s</sub>. Clearly an open hysteresis
loop is observed, whatever the temperature, characteristic of a
ferromagnetic behavior. The saturation is reached at 1 Tesla
and, as expected, the coercive field (*H*<sub>c</sub>) decreases with temp-
erature (300 Oe at 3 K and 70 Oe at 300 K). This clearly con-
firms the ferromagnetic behavior, even at room temperature,
of the 9.2 nm hcp-Co nanocrystals. Furthermore, the reduced
remanence, *M*<sub>r</sub>/*M*<sub>s</sub> = *M*(*H*)/*M*<sub>s</sub> at *H* = 0, is equal to 0.40 and is
in good agreement with the expected value of 0.50 for spheri-
cal nanocrystals having a uniaxial anisotropy,<sup>24,25</sup> which is the
case of hcp-Co NCs. The value expected for spherical NCs with
cubic anisotropy (case of fcc-Co NCs) is 0.83. The lower value
obtained here (0.4 instead 0.5) is due to the surface effect
(spin canting, passivating agent etc.) as generally observed for
magnetic nanoparticles.<sup>26,27</sup> The narrowing of the *M*(*H*) curve
at *H* close to 0 should also be noticed. This effect is often
observed in non-interacting magnetic nanoparticles and
reflects the distribution of magnetic anisotropy mainly due to
the size distribution or to various surface states.<sup>27,28</sup>

As the same nanoparticles are in interaction (i.e. assembled
on a polymeric substrate (adhesive tape) by depositing several
drops of toluene containing solution until complete evapo-

ration), the *M*(*H*) curve is strongly modified as the *H*<sub>c</sub> increases at 3 K to reach 760 Oe at 3 K and 208 Oe at 300 K. This is due to the dipolar interaction, due to the vicinity of the nanocrystals when they are agglomerated on the substrates compared to the case where they are isolated in solution. Furthermore, as the dipolar interactions are long range scale, the narrowing of the *M*(*H*) curve close to *H* = 0 is no more observed. This confirms the weakness of the magnetic interaction in the case of isolated cobalt NCs in solution.

We next studied if it was possible to tune the shape and the
size of the cobalt NPs by varying simple parameters such as
the concentration and reaction time. Reducing the concen-
tration by a factor of two with the same temperature, 190 °C,
and reaction time, 1 h, led to the formation of 7.8 nm Co NCs
(6% of polydispersity) (see ESI Fig. S3A and B†). Crystallinity
characterization proved that these smaller particles are also
hcp-Co NPs (see ESI Fig. S2C†). Surprisingly,²⁹ increasing the
concentration (by a factor 2) did not allow the formation of
bigger hcp-NPs. Formation of hcp-Co NPs of 9.1 nm was
observed, suggesting that under such conditions (temperature
and reaction time) a maximum size is reached (see ESI
Fig. S3†). However, changing the reaction time from the stan-
dard conditions (Table 1, entry 2) has a tremendous effect.
Indeed, by increasing the reaction time, a morphological tran-
sition occurs from spheres to rods with different aspects, the
ratio depending on the reaction time (see ESI Fig. S4† and
Fig. 4 after 540 minutes).

The electronic diffraction pattern (Fig. 4B) obtained for a
collection of nanorods (Fig. 4A) consists of 5 diffractions rings.
The rings characterized by 0.22 nm, 0.197 nm, 0.119 nm and
0.107 nm distances correspond to (101), (103) and (112) planes
of the hcp structure of cobalt metal whereas the 0.174 nm dis-
tance can be attributed to the fcc cobalt structure. It has to be
noted that the nanorods are very thin and few rods contribute

<figure><img src="image_12.png" /><figcaption>Fig. 4 Structural characterization of cobalt nanorods (A) TEM image of cobalt nanorods, (B) electronic diffraction of cobalt nanorods, (C, D) HRTEM image and corresponding FFT (E).</figcaption></figure>

<figure><img src="image_13.png" /></figure>
<figure><img src="image_14.png" /><figcaption>Fig. 5 M(H) curve obtained for Co nanorods isolated in solution measured at 3 K (black line) and 300 K (red line).</figcaption></figure>

to the electronic diffraction explaining the discrete diffuse rings consisting of spots. The HRTEM image of individual nanorods exhibits 3 different lattice planes (Fig. 4C and D). It is well illustrated in the calculated power spectra (Fig. 4E) which have three reflection pairs labeled 1, 2 and 3 characterized by distances $d_1 = 0.215$ nm $\approx d_2 = 0.216$ nm and $d_3 = 0.141$ nm corresponding to the {100} and {102} reflections of the hcp structure. However, in that case the crystal orientation is not clear at all. To further understand this unexpected morphological transition, wide angle and small angle X-ray scattering studies are in progress. Again, the magnetic characterization of isolated nanorods has been performed and a hysteresis loop is observed both at 300 K and 3 K, which confirms the presence of ferromagnetic nanorods. The coercive field, $H_c$ as already observed, decreases with temperature (380 Oe at 3 K and 60 Oe at 300 K). The reduced remanence at 3 K is found to be equal to 0.7, when it decreases to 0.4 at 300 K. The higher value of $M_r/M_s$ observed at 3 K for these uniaxial nanocrystals, compared to the expected value of 0.5 (ref. 24) or to the value obtained for the spherical NCs (0.4), could be due to a partial alignment of the nanorods with the applied magnetic field, when they are isolated in solution and thus allow one to move to follow the magnetic field.30 Thus, magnetic measurements clearly confirm the uniaxial anisotropy of the nanorods (Fig. 5).

## Conclusions

In conclusion we described herein a one-pot synthesis of hcp-cobalt NCs using the simple combination of an easily accessible well-defined cobalt(I) complex [ClCo(PPh₃)₃] and oleylamine. The resulting NCs have been well characterized and clearly are ferromagnetic at room temperature. This new scalable synthesis allows one to control the size and the shape of magnetic nanocrystals depending only on the reaction conditions (time, concentration etc.). From an economical point of view, the obtention of a solution containing shape- and size-controlled ferromagnetic hcp-cobalt NCs opens a wide range of applications. Mechanistic studies for the formation of the NCs and the morphological transition are under progress.

## Acknowledgements

This work was supported by CNRS, MRES, UPMC and by the LabEx MiChem, part of French state funds managed by the ANR within the "Investissements d'Avenir" program under reference ANR-11-IDEX-0004-02 which we gratefully acknowledge. The subject matter described in the present article is covered by a patent application no. FR1562083.

## Notes and references

1. (a) N. A. Frey, S. Peng, K. Cheng and S. Sun, *Chem. Soc. Rev.*, 2009, **38**, 2532; (b) K. Khan, S. Rehman, H. U. Rahman and Q. Khan, *Synthesis and application of magnetic nanoparticles*, in *Nanomagnetism*, ed. J. M. Gonzalez Estevez, One Central Press (OCP), UK, 2014, p. 135; (c) Z. Nie, A. Petukhova and E. Kumacheva, *Nat. Nanotechnol.*, 2010, 5, 15.

2. (a) K. M. Krisna, A. B. Pakomov, Y. Bao, P. Blomqvist, Y. Chun, M. Gonzales, K. Griffin, X. Ji and B. K. Roberts, *J. Mater. Sci.*, 2006, **41**, 793; (b) C. Sun, J. S. Lee and M. Zhang, *Adv. Drug Delivery Rev.*, 2008, **60**, 1252; (c) F. Sonvico, S. Mornet, S. Vasseur, C. Dubernet, D. Jaillard, J. Degrouard, J. Hoebeke, E. Duguet, P. Colombo and P. Couvreur, *Bioconjugate Chem.*, 2005, **16**, 1181.

3. (a) L. Yong, L. Qiying and S. Wenjie, *Dalton Trans.*, 2011, **40**, 5811; (b) L. L. Chng, N. Erathodiyil and J. Y. Ying, *Acc. Chem. Res.*, 2013, **46**, 1825; (c) A. Y. Khodakov, W. Chu and P. Fongarland, *Chem. Rev.*, 2007, **107**, 169; (d) S. W. Kim, S. U. Son, S. S. Lee, T. Hyeon and Y. K. Chung, *Chem. Commun.*, 2001, 2212.

4. (a) N. A. Frey and S. Sun, Magnetic Nanoparticle for Information Storage Applications, in *Inorganic Nanoparticles: Synthesis, Applications, and Perspectives*, ed. C. Altavilla and E. Ciliberto, CRC Press, 2010; (b) G. C. Papaeftymiou, *Nano Today*, 2009, **4**, 438; (c) A.-H. Lu, E. L. Salabas and F. Schuth, *Angew. Chem., Int. Ed.*, 2007, **46**, 1222; (d) S. Karmakar, S. Kumar, R. Rinaldi and G. Maruccio, *J. Phys.: Conf. Ser.*, 2011, **292**, 012002.

5. B. Podmiljsak, P. J. McGuiness, N. Mattern, H. Ehrenberg and S. Kobe, *IEEE Trans. Magn.*, 2009, **45**, 4364.

6. P. Gambardella, S. Rusponi, M. Veronese, D. Dhesi, C. Grazioli, A. Dallmeyer, I. Cabria, R. Zeller, P. H. Dederichs, K. Kern, C. Carbone and H. Brune, *Science*, 2003, **300**, 1130.

7. C. P. Gibson and K. J. Putzer, *Science*, 1995, **267**, 1338.

8. (a) F. Fievet, J. P. Lagier, B. Blin, B. Beaudoin and M. Figlarz, *Solid State Ionics*, 1989, **32/33**, 198; (b) F. Boneta, V. Delmasa, S. Grugeona, R. H. Urbina, P. Y. Silverta and K. Tekaia-Elhsissena, *Nanostruct. Mater*, 1999, **11**, 1277; (c) D. Larcher and R. J. Patrice, *Solid State Chem.*, 2000, **154**, 405.

9. (a) R. J. Joseyphus, T. Matsumoto, H. Takahashi, D. Kodama, K. Tohji and B. J. Jeyadevan, *Solid State Chem.*,

<figure><img src="image_15.png" /></figure>
2007, **180**, 3008; (b) C. W. Kim, H. G. Cha, Y. H. Kim, A. P. Jadhav, E. S. Ji and D. I. Kang, *J. Phys. Chem. C*, 2009, **113**, 5081; (c) S. I. Cha, C. B. Mo, K. T. Kim and S. H. Hong, *J. Mater. Res.*, 2005, **20**, 2148; (d) Y. Soumare, C. Garcia, T. Maurer, G. Chaboussant, F. Ott, F. Fiévet, J.-Y. Piquemal and G. Viau, *Adv. Funct. Mater.*, 2009, **19**, 1971.

10 (a) F. S. Diana, S. H. Lee, P. M. Petroff and E. J. Kramer, *Nano Lett.*, 2003, **3**, 891; (b) V. F. Puntes, K. M. Krishnan and A. P. Alivisatos, *Science*, 2001, **291**, 2115; (c) Y. Bao, W. An, C. Health Turner and K. M. Krishnan, *Langmuir*, 2010, **26**(1), 478.

11 V. F. Puntes, D. Zanchet, C. K. Erdonmez and A. P. Alivisatos, *J. Am. Chem. Soc.*, 2002, **124**, 12874.

12 F. Dassenoy, M.-J. Casanove, P. Lecante, M. Verelst, E. Snoeck, A. Mosset, T. Ould Ely, C. Amiens and B. Chaudret, *J. Chem. Phys.*, 2000, **112**, 8137.

13 F. Dumestre, B. Chaudret, C. Amiens, M. C. Fromen, M. J. Casanove, P. Renaud and P. Zurcher, *Angew. Chem., Int. Ed.*, 2002, **41**, 4286.

14 M. Comesaña-Hermo, R. Estivill, D. Ciuculescu, Z.-A. Li, M. Spasova, M. Farle and C. Amiens, *Langmuir*, 2014, **30**, 4474.

15 (a) A. Demortière and C. Petit, *J. Appl. Phys.*, 2012, **109**, 084344; (b) S. Sun and C. B. Murray, *J. Appl. Phys.*, 1999, **85**, 4325.

16 (a) S. Mourdikoudis and M. L. Liz-Marzań, *Chem. Mater.*, 2013, **25**, 1465; (b) Y. Yu, W. Yang, X. Sun, W. Zhu, X.-Z. Li, D. J. Sellmyer and S. Sun, *Nano Lett.*, 2014, **14**(5), 2778.

17 B. Cormary, F. Dumestre, N. Liakakos, K. Soulantica and B. Chaudret, *Dalton Trans.*, 2013, **42**, 12546.

18 H. Brune, A. Court, C. Petit and V. Repain, *Self-Assembly of Nanoalloys*, in *Nanoalloys: From Fundamentals to Emergent Applications*, ed. F. Calvo, Elsevier, 2013, p. 373.

19 (a) M.-P. Pileni, *Acc. Chem. Res.*, 2008, **41**, 1799-1809; (b) B. L. V. Prasad, C. M. Sorensen and K. J. Klabunde, *Chem. Soc. Rev.*, 2008, **37**, 1871-1883; (c) S. I. Stoeva, B. L. V. Prasad, S. Uma, P. K. Stoimenov, V. Zaikovski, C. M. Sorensen and K. J. Klabunde, *J. Phys. Chem. B*, 2003, **107**, 7441-7448.

20 J. Richardi and J. J. Weis, *J. Chem. Phys.*, 2013, **138**, 244704.

21 D. Talapin, E. V. Shevchenko, C. B. Murray, A. V. Titov and P. Kraal, *Nano Lett.*, 2007, **7**, 1213-1219.

22 A. P. Guimaraes, in *Principles of Nanomagnetism*, Springer, 2009, p. 68.

23 M. Walker, P. I. Mayo, K. O'Grady, S. W. Charles and R. W. Chantrell, *J. Phys.: Condens. Matter*, 1993, **5**, 2779.

24 E. C. Stoner and E. P. Wohlfarth, *IEEE Trans. Magn.*, 1991, **27**, 3475.

25 I. Joffe and R. Heuberger, *Philos. Mag.*, 1974, **314**, 1051.

26 J. P. Chen, C. M. Sorensen, K. J. Klabunde, G. C. Hadjipanayis, E. Devlin and A. Kostikas, *Phys. Rev. B: Condens. Matter*, 1996, **54**, 9288.

27 C. Vázquez-Vázquez, M. A. López-Quintela, M. C. Buján-Núñez and J. Rivas, *J. Nanopart. Res*, 2011, **13**, 1663.

28 R. Morel, A. Brenac, C. Portemont, T. Deutsch and L. Notin, *J. Magn. Magn. Mater.*, 2007, **308**, 296.

29 A. T. Ngo and M. P. Pileni, *J. Appl. Phys.*, 2002, **92**, 4649.

30 C. B. Williamson, D. R. Nevers, T. Hanrath and R. D. Robinson, *J. Am. Chem. Soc.*, 2015, **137**, 15843.