# Magnetic properties of 2D nickel nanostrips: structure dependent magnetic anomaly

###### Abstract

We have investigated different geometries of two dimensional (2D) infinite length Ni nanowires of increasing width using spin density functional theory calculations. Our simulations demonstrate that the parallelogram motif is the most stable and structures that incorporate the parallelogram motif are more stable as compared to rectangular structures. The wires are conducting and the conductance channels increase with increasing width. The wires have a non-linear behavior in the ballistic anistropic magnetoresistance ratios with respect to the magnetization directions. All 2D nanowires as well as Ni (111) and Ni (100) monolayer investigated are ferromagnetic under the Stoner criterion and exhibit enhanced magnetic moments as compared to bulk Ni and the respective Ni monolayers. The Stoner parameter is seen to depend on the structure and the dimension of the Nws. The easy axis for all nickel nanowires under investigation is observed to be along the wire axis. The double rectangular nanowire exhibits a magnetic anomaly with a smaller magnetic moment when compared to Ni (100) monolayer and is the only structure with an easy axis perpendicular to the wire axis.

###### pacs:

31.15.E-,73.63.-b,75.75.-c,75.30.Gw## I Introduction

Magnetism in nanoscale films is an exciting area of research, as their magnetic behavior is different than that observed in bulk. The applications of magnetic materials are mostly determined by the softness or hardness of the magnet. The soft magnets with low coercivities are used for flux guidance in permanent magnets and in transformer cores for high frequency and microwave applications.Tung and Guo (2007); Skomski (2008) In hard magnets, knowledge of the easy direction of magnetization and magnetic anisotropy energy is necessary for high density recording devices such as memories and magnetic tapes in audio-visual technology. Tung and Guo (2007); Skomski (2008) The magnetic properties of materials in the nanoscale regime are quite interesting as they show enhanced magnetic moments due to the reduced coordination, and exhibit magnetic anisotropy due to symmetry breaking.

Nickel is one of the most investigated materials, for its magnetic properties and its applicability in material science. The magnetic properties of bulk nickel,Doll (2003); Smogunov et al. (2003a); Krutzen and Springelkamp (1989); Brookes et al. (1992); Borgiel and Nolting (1990); Zarechnaya et al. (2008) Ni surfacesWimmer et al. (1984); Freeman et al. (1982); Freeman and Wu (1991); Bennett and Cooper (1971); Takayama et al. (1976); Krakauer et al. (1983); Jepsen et al. (1982) and layersZhu and Hermanson (1983); Tersoff and Falicov (1982); Li et al. (1990); Pick and Dreyssé (1992); Freeman and Wu (1991); Gay and Richter (1986) have been investigated in great detail. Single atom linear chains and zigzag nanowires (Nws) of Ni have been studied earlier for their stability.Zelený et al. (2009); Tung and Guo (2007); Sabirianov (2006); Smogunov et al. (2003a, 2004a); Smogunov et al. (2002); Ooka et al. (2001); Wernsdorfer et al. (2005); Ataca et al. (2008) The investigations by Tung et al., on the magnetic properties of all 3 transition elements have found that in Ni the linear and zigzag wires are ferromagnetic. In a recent work, Zelený et al.,Zelený et al. (2009) have investigated systematically the variation in structural and magnetic properties of one dimensional nanowires, two dimensional strips and three dimensional rods, under compression. The compressed two dimensional (2D) Ni nanowires have a ferromagnetic ground state, because of magnetic shape anisotropyTung and Guo (2007); Zelený et al. (2009). This result contradicts the work of Mermin-WagnerMermin and Wagner (1966), which showed that, one and two dimensional structures cannot exhibit ferromagnetic or antiferromagnetic behavior, under the isotropic Heisenberg model. Clearly, the magnetic anisotropy plays a crucial role which needs to be understood and investigated for a fundamental understanding of the magnetic behavior and its dependence on the structure. The magnetic anisotropy in low dimensional chains is seen to exhibit significantly different behavior than bulk.Tung and Guo (2007) The results for linear (viz., V, Cr and Fe) as well as zigzag (Cr, Mn and Co) transition metal chains show that these systems show stable axial magnetic anisotropy energy, with large magnitude in comparison with that of bulk. It was also observed that, the magnetic anisotropy energy especially, shape anisotropy energy was sensitive to the atomic arrangement of the nanowires even in low dimension. These results highlight the strong impact of magnetic anisotropy energy on the magnetic ground state of low dimensional material. Nanowires with very strong magnetic anisotropy with the magnetic moments in the ferromagnetic order have potential applications in ultrahigh density magnetic memories and storage devices.Tung and Guo (2007) Hence, the relationship between magnetic anisotropy energy and the geometrical structure of the atomic chains with gradually varying atomic width will be interesting for basic understanding as well as for specific applications in devices. This kind of an investigation is not available either theoretically or experimentally for 2D nanostrips. In addition to the magnetic ground state, the magnetic anisotropy and hence the direction of the magnetic moments has a significant effect on the ballistic conductance in magnetic nanowires. The experimentally observed ballistic conductance in linear Ni Nws was successfully explained by considering the magnetic domain formation over uniform magnetic moments.Smogunov et al. (2004b); Smogunov et al. (2002); Ooka et al. (2001); Sirvent et al. (1996); Li et al. (2007); García-Mochales et al. (2005, 2008) The exact effect of orientation of the magnetic moment with respect to the current direction on the ballistic conductance in the linear Ni Nw was demonstrated by Velev et al,Velev et al. (2005) and it was found that changing the direction of the magnetic moment either perpendicular or parallel to the current direction enhances the ballistic conductance upto 14%. Hence, it will be very interesting to investigate the effect of the direction of the magnetic moment on the ballistic conductance of the nanowires with reduced symmetry and larger widths than the linear nanowire.

In the present paper, we have investigated the magnetic and electronic properties of nickel nanowires as their structure varies from a linear chain to two dimensional nanostrips of increasing widths. Besides their stability, we have investigated the effect of the geometrical structure on their magnetic properties. We confirm the ferromagnetic ground state of Ni Nw structures based on Stoner’s criterion. We have studied systematically the the effect of geometrical structure on the spin dependent ballistic conductance. We observe a structure dependence on the value of the Stoner’s integral which is so far known to be a constant for a particular material. The structure of the paper is as follows: Section II gives an overview of computational parameters and methods used. The results on the stability, electronic structure, conductance, magnetic properties and magnetic transition are discussed under Sec. III which is followed by a summary of the work in Sec. IV.

## Ii Computational Details

We have performed total energy calculations based on ab initio spin density functional theory (DFT) as implemented in the Vienna ab initio Simulation Package(VASP) Kresse and Hafner (1993); Kresse and Furthmüller (1996a, b). The Projector Augmented Wave method (PAW) Kresse and Joubert (1999) and the Generalized Gradient Approximation (GGA)Perdew et al. (1992) have been used to describe the electron-ion interactions and the exchange correlation interactions. The details of modeling of such nanowires and the calculation of the binding energy have been described earlier for gold.Kashid et al. (2011) The geometry optimization and the electronic band structure calculations are performed without the scalar relativistic effects, as the investigations on 3 transition metals have demonstrated that the spin orbit coupling energy is approximately 3 times smaller than the exchange splitting in bulk Ni,Wimmer et al. (1984) and hence can be neglected.

The magnetic anisotropy in a magnetic material has contributions from magnetocrystalline anisotropy and magnetic shape anisotropy. In bulk Ni, the shape anisotropy energy does not contribute and the only contribution is from the magnetocrystalline anisotropy. However, in 1D wires and 2D strips, the reduced symmetry of the system gives non-zero contributions to the shape (magnetostatic) anisotropy. The magnetic shape anisotropy is computed based on the magnetic dipolar energy, resulting from the interactions of the magnetic moments with each other. It is given by

(1) |

where, m and m are the magnetic moments at the ionic positions r and r. The vector r is defined as r-r. The magnetic dipolar energy is a long range interaction, hence the value of has been converged over the length of the nanowire by using supercell. The dipolar energy is sensitive to the orientation of the magnetic moments, hence we define magnetic shape anisotropy (MSA) as, and where , and are the classical dipole-dipole interaction energy terms, when the magnetic moments are aligned along , and direction.

For the calculation of the magneto-crystalline anisotropy energy (MCA), we have done self consistent calculations by including the spin orbit coupling and with the magnetization direction oriented along one of the Cartesian axes. We have used the total energy difference method for the calculation of the anisotropy energy (MCA) due to the orientation of the magnetization along the different directions. We have defined = E-E, and =E-E, where, is the periodic wire direction, is the perpendicular direction in the plane of the wire and is perpendicular to both the wire axis and the wire plane. The total magnetic anisotropy (MAE) is calculated as, .

In order to understand the electronic and conduction properties of the nanowires, we have performed band structure analysis as described by Kashid et al. Kashid et al. (2011) The conducting properties of nickel nanowires are investigated based on the Landuaer-Büttiker formalism, Imry and Landauer (1999) using the method of plane waves. Oetzel et al. (2008); Treske et al. (2010) For ideal infinite length nanostrips, the ballistic conductance () can be written as,

(2) |

where, represents the quantization unit of conductance, in the case of spin degeneracy. The term shows the number of conductance channels, and it is explicitly calculated by counting the number of bands crossing the Fermi energy E). For ferromagnetic nanowire, the conductance is expected to exhibit spin dependence, where spin up () and spin down () electrons contribute independently to the number of conductance channels.Ooka et al. (2001) Hence Eq. 2 can be modified for ferromagnetic nanowires as,

(3) |

where, is the number of spin up (down) bands at the Fermi energy.
The effect of spin orbit coupling (SOC) on the conduction in Ni Nws has been investigated based on the ballistic anisotropic magnetoresistance () computation described by Velev et al.Velev et al. (2005) We have calculated the percentage as,

(4) |

where is the total number of conducting channels, when the magnetization is perpendicular to the current direction (axial direction) and is the number of conducting channels, when the magnetization is parallel to the axial direction.
The two anisotropic magnetization directions viz., and that are perpendicular to the current direction give different percentage BAMR denoted by A (B), respectively.

We have used the Stoner’s model of ferromagnetism to determine the appearance of ferromagnetic ground state in Ni Nws. The product satisfying defines the system as ferromagnetic, where is the Stoner exchange parameter, obtained from . The defines the exchange splitting between majority and minority spin electrons due to magnetization, and is calculated directly from the total density of states (DOS) of nickel nanowires. The quantity denotes the magnetic moment per atom, whereas denotes the normalized DOS (DOS per atom per spin) at the Fermi energy () of the nonmagnetic calculation.

## Iii Results and Discussion

### iii.1 Structure and stability

We have investigated different geometries of Ni nanostrips of widths upto 1 nm approximately. Figure 1 shows the optimized geometries of nickel nanowires arranged according to increasing number of rows. In each row, the structures are arranged in the ascending order of stability. The bond lengths between nickel atoms in the unit cell of each nanowire are displayed in Fig. 1. Linear Ni nanowire (Fig. 1a(i)) has been investigated earlier in detailZarechnaya et al. (2008); Tung and Guo (2007); Smogunov et al. (2004b); Ooka et al. (2001); Wen et al. (2005); Li et al. (2007); Smogunov et al. (2003b) and we report it for comparison with the magnetic properties of increasing width nanostrips. Our bond length of 2.17 Å is in good agreement with the calculations of Zelený et al. Zelený et al. (2009) Like gold Nws, infinite length linear Ni nanowire does not exhibit dimerization in bond lengths.Kashid et al. (2011)

Geometry | Number | Width | Bonding Factor | Magnetization | Conduction | channels |
---|---|---|---|---|---|---|

of rows | (nm) | (bonds/atom) | /atom) | () | () | |

Linear (LR) | 1.00 | 1 | 6 | |||

Rectangular (RT-1) | 1.50 | 2 | 6 | |||

Parallelogram (PR-1) | 2.00 | 2 | 6 | |||

Rhombus (RH) | 1.33 | 1 | 3 | |||

Double rectangular (RT-2) | 1.66 | 3 | 7 | |||

Pentagonal (PNT) | 2.00 | 2 | 6 | |||

Double parallelogram (PR-2) | 2.33 | 2 | 5 | |||

Triple rectangular (RT-3) | 1.75 | 4 | 9 | |||

Hexagonal (HX) | 2.25 | 3 | 7 | |||

Triple parallelogram (PR-3) | 2.50 | 3 | 10 | |||

Centered hexagonal (CHX-1) | 2.20 | 2 | 6 | |||

Quadruple rectangular (RT-4) | 1.83 | 5 | 12 | |||

Hexagonal type-I (HX-T1) | 2.20 | 4 | 12 | |||

Hexagonal type-II (HX-T2) | 2.39 | 4 | 12 | |||

Quadruple parallelogram (PR-4) | 2.60 | 4 | 13 | |||

Quintuple rectangular (RT-5) | 1.80 | 6 | 17 | |||

Centered hexagonal-II (CHX-2) | 2.16 | 3 | 4 | |||

Quintuple parallelogram (PR-5) | 2.66 | 4 | 12 | |||

Bulk nickel |

In the double row Nws, nickel forms either rectangular or parallelogram structure.
Our investigations show that, unlike gold nanowires (GNWs), Ni Nws show a single minima in the double row parallelogram structure, which consists of all acute angle triangles.
The double row parallelogram and rectangular structure form the basic building blocks for all subsequent higher row structures.
The important difference between GNWs and Ni Nws is that, the metastable structures like zigzag (ZZ), hexagonal (HX), double zigzag (DZZ) in GNWs are not observed in Ni Nws.
The optimization of these structures leads to more stable PR-1 and HX structure (that is formed of a rectangular structure sandwiched between two parallelogram structures).
In the present work, we have investigated additional structures like HX-T1 and HX-T2 (Fig. 1e(iii) and Fig. 1e(iv) respectively), which are formed by different combinations of rectangular and parallelogram structures.
HX-T1 consists of an alternate parallelogram and rectangular row of Ni atoms along the Y direction, whereas, in the HX-T2 case, the topmost rectangular row is replaced by a parallelogram row.
These additional structures assist to understand that, the stability in Ni NWs is strongly dependent on the geometrical arrangement of Ni atoms.
All rectangular nanowires show a bond length of 2.25 Å along the periodic direction except for RT-2 structure which has a 2.26 Å bond length.
The parallelogram nanowires have slightly enhanced bond lengths of 2.30 Å for PR-1, PR-2, 2.33 Å for PR-3, PR-4, and 2.34 Å for PR-5 structure, in comparison with that of rectangular nanowires. These bond lengths are converging to 2.26 Å and 2.36 Å, respectivelythe single layered limit for Ni (100) and Ni (111) films.
The rectangular and parallelogram nanowires show dimerization in bond lengths along the nonperiodic direction, similar to that observed in GNWs.Kashid et al. (2011)
The dimerization in bondlengths is observed for nanowire structures made up of 4 or more rows of nickel
atoms and it is symmetric from the center of the structure along the nonperiodic Y direction.

Figure 2 shows the plot of the calculated binding energies per atom as a function of number of rows,
for each nanowire investigated. In general, as the width of the nanostrips
increases the stability of the structures increases. The parallelogram shaped nanowires are the most
stable structures within a particular number of rows. Nanowires formed via a combination of parallelogram
and rectangular motifs are stable over pure rectangular shaped structures. The energy difference between rectangular shaped and parallelogram shaped structures, is small at smaller widths, however, the difference increases with an increase in the width. Our calculations show that a single layer parallelogram film is
more stable than rectangular film by 0.34 eV/atom. This increase in the energy difference between rectangular and parallelogram nanowires with increasing number of rows was observed previously in the case of GNWs.Kashid et al. (2011)
The energy difference between rhombus and rectangular wires is large for 3 rows, however, the difference reduces with increasing number of rows and crossover in stability is observed at 6 rows.
The rhombus structure and rectangular structures are the least stable. The structures that incorporate parallelograms are energetically more preferred. The HX-T2 structure with more rows of parallelograms is
stable over HX-T1 structure. The binding energies of the rectangular and parallelogram shaped nanowires are converging to their
calculated single layered film limit of –3.34 eV/atom and –3.68 eV/atom, respectively.

Rows | site | Rectangular Wires | Parallelogram Wires | ||||||
---|---|---|---|---|---|---|---|---|---|

in Nws | total | total | |||||||

1 | T | 0.55 | 0.15 | 8.33 | 9.03 | 0.55 | 0.15 | 0.83 | 9.03 |

2 | T | 0.54 | 0.23 | 8.35 | 9.12 | 0.53 | 0.25 | 8.35 | 9.12 |

3 | T | 0.54 | 0.21 | 8.37 | 9.12 | 0.54 | 0.22 | 8.36 | 9.12 |

C | 0.54 | 0.34 | 8.34 | 9.22 | 0.54 | 0.39 | 8.31 | 9.24 | |

4 | T | 0.54 | 0.21 | 8.36 | 9.11 | 0.54 | 0.22 | 8.35 | 9.11 |

C | 0.54 | 0.32 | 8.35 | 9.21 | 0.55 | 0.38 | 8.30 | 9.23 | |

5 | T | 0.54 | 0.21 | 8.36 | 9.11 | 0.54 | 0.22 | 8.35 | 9.11 |

I | 0.54 | 0.32 | 8.34 | 9.19 | 0.55 | 0.37 | 8.30 | 9.23 | |

C | 0.53 | 0.30 | 8.35 | 9.18 | 0.56 | 0.37 | 8.31 | 9.23 | |

6 | T | 0.54 | 0.21 | 8.35 | 9.10 | 0.54 | 0.22 | 8.35 | 9.11 |

I | 0.54 | 0.32 | 8.34 | 9.20 | 0.55 | 0.37 | 8.31 | 9.22 | |

C | 0.54 | 0.30 | 8.35 | 9.18 | 0.56 | 0.35 | 8.31 | 9.22 |

In order to understand the stability of the nanowires, we have calculated the average number of nearest neighbors in each structure and listed them as bonding factor in Table-1, along with the number of rows and the width of the structure. The higher stability of parallelogram Nws in any row can be attributed to their higher bonding factor (or largest number of nearest neighbors) in comparison with the other structures that have the same number of rows. In addition, we have also analyzed the decomposition of total charge in the parallelogram and rectangular structures and listed their l-projected components in Table 2 along with that of the linear wire for comparison. The values of the charges are listed for the atoms along the -direction from the vacuum end to the center of the nanowire. The atomic sites for the terminal row, intermediate row and central row atoms are labeled as ‘T’, ‘I’ and ‘C’, as shown in Fig. 1. It is observed that the least coordinated linear structure has the least amount of charge in orbitals as compared to that in all the higher width Nws. Adding one row of Ni atoms to the linear wire structure, increases the electron occupation in orbitals of the terminal atoms to 0.08 and 0.10 for the rectangular and parallelogram Nws, respectively.

For all the Nws with number of rows 3, the increased coordination of the ‘I’ and ‘C’ kind of atoms enhances the orbital occupancy. In the rectangular shaped nanowires with 5 and 6 rows of atoms, the central atoms loose some of their charge to the interstitial region, thus reducing the total charge of the ‘C’ atoms. Interestingly, the ‘I’ atoms of 5 and 6 row rectangular atoms show more total charge than ‘T’ and ‘C’ atoms. The ‘C’ atoms of 5 and 6 row loose more charge to the vacuum in comparison with ‘I’ atom, although both have the same coordination, unlike that of the parallelogram Nws of the same number of rows. In parallelogram Nws, only the terminal row atoms are affected by the metal-vacuum interface in the XY-plane and all sub-terminal atoms (‘I’ and ‘C’ type) have essentially unchanged total charge. This reduction in charge of the ‘T’ atoms at the metal vacuum interface of two dimensional films is analogous to the loss of charge by the surface atoms observed by Wimmer et al. for a 7 layer slab of Ni (001).Wimmer et al. (1984) Our results demonstrate that the metal vacuum interface has the largest effect on the orbital electron distribution. Increase in total charge on an atom in parallelogram Nws is because of the increase in contribution. This increase in total charge as compared to that of rectangular Nws enhances the stability of parallelogram Nws. We believe this stability preference will be retained in nanowires deposited on surface.

### iii.2 Electronic structure and conductance

We have calculated the spin-dependent electronic energy band structure (BS) and density of states (DOS) of all the nanowires to study their electronic and conducting properties. As the number of rows in the Nws is increased, the states are increasingly delocalized leading to an increase in the stability of the nanowires of increasing widths. In all the Nws investigated here, the 3, 4 and 4 states hybridize, so that all the spin up states are filled, while the spin down states are left unfilled. The spin dependent band structure shows large number of unfilled spin down energy bands in comparison with the spin up bands at the Fermi level. In the spin up band structure, the orbital bands are approximately 0.5 eV below the Fermi level. The fat band analysis of the spin up band structures of all nickel nanowires shows contributions at the Fermi energy from , and orbitals. The contributions from the states are large in comparison with the contributions from the states. Amongst the states, contributes strongly and has minor contributions in the rectangular Nws. In parallelogram Nws, the orbitals are filled, pulled below the Fermi level and contributes strongly at the Fermi level. In rectangular nanowires as the number of rows is increased, the states extend beyond the Fermi energy leaving them increasingly unfilled. As the number of rows in parallelogram nanowires is increased, the orbitals become more delocalized and their contribution to the spin up states increases. Our analysis from the partial DOS reveals that this increased contribution is from the atoms in the inner rows of the Nw structure. The terminal rows of atoms do not give significant contribution from the orbital. As the coordination of the atoms in the nanowires increases with increasing widths, the and orbitals give enhanced contributions in spin up bands, which assists to increase the stability of the nanowires. On the other hand, in the spin down energy band structures, all the orbitals show dominant contributions along with the orbital at the Fermi level. The hybridized spin down energy levels have less contributions from the electrons.

The conductance in nickel nanowires was calculated using Landauer formulaImry and Landauer (1999) (Eq. 2 and Eq. 3). Our calculated values of conductance in all nickel nanowire are listed in Table 1 for spin up and spin down channels. The less stable nanowires show higher conductance than the more stable nanowires, in agreement with the conductance behavior in Au Nws. All rectangular nanowires with rows 2 have enhanced number of conduction channels than that of parallelogram nanowires. The enhanced conductance in rectangular Nws in comparison with parallelogram Nws was also observed in Au nanowires.Kashid et al. (2011) All rectangular nanowires show a consistent increment in the total number of (spin up and spin down) conduction channels with an increase in the width of the nanowires. However, the parallelogram Nws show a very small increase in total number of conduction channels as the width increases. It must be noted that in all Nws, there is not a significant increment in the number of spin up channels as the number of rows is increased, however, there is a large enhancement in the number of spin down conduction channels. In agreement with earlier calculations,Smogunov et al. (2002) the charge carriers in spin up conductance channels are mainly type and in spin down conductance channels the charge carriers are mostly type with minor contributions from type.

### iii.3 Magnetic Properties

#### iii.3.1 Magnetic moment

Earlier studies on Ni surfaces have shown that (111) films of layers are ferromagnetic, whereas films of layers show a paramagnetic behavior.Bergmann (1978); Pourovskii et al. (1999) This raises an interesting question, what is the effect of the width and structure of single layered nanostrips on their magnetic properties? With this aim, we have investigated the magnetic properties of Ni Nws and compared them with Ni monolayers. The calculated magnetic moments of the Nws are listed in Table 1. As expected, in nanostructures with reduced coordination, all Nws have enhanced magnetic moments in comparison with that of the bulk. The linear wire with the least coordination has the largest magnetic moment and the magnetic moments decrease with minor fluctuations as the widths of the nanostrips increase. A comparison of the magnetic moments of the rectangular and parallelogram shaped wires is plotted in Fig. 3, and it shows that the magnetic behavior of these wires is considerably different. In the rectangular wires, the magnetic moments initially decrease and then increase again. Interestingly, the triple row RT-2 structure, has a magnetic moment of 0.81 /atom, which is less than the magnetic moments of other higher row rectangular structures as well as that of the Ni (100) monolayer. Our calculated magnetization of 0.83 /atom for a (100) monolayer film, is in good agreement with 0.86 /atom of (100) monolayer.Freeman et al. (1982) The magnetic behavior of RT-2 is unusual when compared to the observation that magnetic moments increase as the atomic coordination decreases. We find that the “magic structure” RT-2 has an uncommon behavior in all the magnetic aspects analyzed. The parallelogram shaped wires exhibit an initial sharp decrease and then the magnetic moments decrease very gradually with small fluctuations. The six row parallelogram structure (PR-5) has a magnetization of 0.85 /atom, which is larger than the calculated (111) film value of 0.79 /atom. Our calculated bulk magnetization value of 0.62 /atom is in good agreement with the earlier reports.Freeman et al. (1982); Zhu and Hermanson (1983); Dal Corso and de Gironcoli (2000); Tersoff and Falicov (1982)

The values of decomposed magnetic moments for all symmetric atoms (described as ‘T’, ‘I’ and ‘C’ in the previous subsection) in rectangular and parallelogram Nws are listed in Table-3. As expected for magnetic systems, the difference in the contributions from spin up orbitals and the spin down orbitals, gives rise to the spin imbalance in Nws. However, the spin imbalance in the Nws is also dictated by the polarization of and orbitals and their contributions in addition to that of the contributions of the orbitals. The variations in the magnetic moments (Table-1) of the Nw structures investigated arise from the amount of slightly negative polarization of delocalized and/or orbitals which is listed in Table-3. Linear Nw has the largest spin imbalance in and orbitals amongst the 2D structures we investigated, and this accounts for its large net magnetization. We notice that, all rectangular nanowires show a small negative polarization. The unusual magnetic behavior of RT-2 is on account of it being the only rectangular Nw with a negative polarization in addition to the negative polarization. The contributions from the orbitals decrease until the 3 row “magic structure” and then increase again as the number of rows in the Nws are increased. Hence, the magnetic moments show an initial decrease and then increase again as the number of rows is increased, in rectangular nanowires. The increased coordination of the ‘C’ type of atoms with an increase in the number of rows, reduces their magnetic moments. Increment in the coordination saturates slowly as the number of rows is increased, and hence magnetization values converge slowly to their single film limit.

The parallelogram Nws with rows of atoms, show negative polarization in the and orbitals of atoms in the non terminal rows. The amount of the negative polarization in the Nws is symmetric about the center of the nanowire and decreases slightly as the number of rows is increased. The contributions do not change as the number of rows is increased and hence the total magnetic moment of atoms in parallelogram shaped wires decreases with an increase in the number of rows of atoms. Although, the negative polarization of and orbitals is significantly smaller in value, in comparison with the positive polarization of orbitals, it plays a significant role in the magnetic behavior of the parallelogram Nws. The increased coordination of ‘I’ and ‘C’ type of atoms leads to a decrease in the charge differences in majority and minority spins, thus, reducing their magnetic moments. In addition, the negative and polarization of the ‘I’ and ‘C’ (Table-3) atoms although small, reduces the total spin imbalance, resulting in the reduction of net magnetization. As a result, the parallelogram Nws show decreased magnetization as the number of rows is increased. The negative polarization of ‘I’ and ‘C’ atoms in rectangular Nws ( and ) is smaller in comparison with that of parallelogram Nws ( and ) (Table-3). This enhances the net magnetic moment of atoms in rectangular nanowires in comparison with parallelogram Nws.

Rows | site | Rectangular Wires | Parallelogram Wires | ||||||
---|---|---|---|---|---|---|---|---|---|

in Nws | total | total | |||||||

1 | T | 0.03 | 0.00 | 1.08 | 1.11 | 0.03 | 0.00 | 1.08 | 1.11 |

2 | T | 0.00 | 0.00 | 0.90 | 0.89 | 0.01 | 0.00 | 0.89 | 0.90 |

3 | T | 0.01 | -0.01 | 0.84 | 0.84 | 0.00 | -0.01 | 0.87 | 0.86 |

C | -0.01 | -0.01 | 0.91 | 0.89 | -0.01 | -0.03 | 0.89 | 0.85 | |

4 | T | 0.01 | -0.01 | 0.87 | 0.86 | 0.00 | 0.00 | 0.89 | 0.89 |

C | 0.00 | -0.01 | 0.85 | 0.84 | -0.01 | -0.03 | 0.89 | 0.86 | |

5 | T | 0.01 | -0.01 | 0.89 | 0.89 | 0.01 | 0.00 | 0.89 | 0.90 |

I | 0.00 | -0.01 | 0.89 | 0.88 | -0.01 | -0.02 | 0.89 | 0.86 | |

C | 0.01 | -0.00 | 0.84 | 0.86 | -0.01 | -0.02 | 0.84 | 0.80 | |

6 | T | 0.01 | -0.01 | 0.90 | 0.90 | 0.01 | 0.00 | 0.89 | 0.90 |

I | 0.00 | -0.01 | 0.90 | 0.89 | -0.01 | -0.02 | 0.89 | 0.86 | |

C | 0.01 | 0.00 | 0.85 | 0.86 | -0.01 | -0.02 | 0.84 | 0.80 |

In RT-2 Nw, the ‘C’ atom, besides being more coordinated than ‘T’ atom, gives large spin imbalance due to states. This spin imbalance due to states in RT-2 Nw enhances the net magnetic moment of the atoms belonging to the central row. This is the only structure, whose terminal atoms show reduced magnetic moments in comparison with the magnetic moment of the central atom. This reduction is similar to the reduction in the magnetic moments of surface atoms reported earlier for Ni (001) multilayer slabs, with existence of “magnetically dead layers”.Liebermann et al. (1970) In RT-2 structure, the resultant magnetic moment due to ‘C’ and ‘T’ atoms gives large dip in the magnetization curve (plotted in Fig. 3).

The spin density (not shown here) of the terminal row atoms have significant contribution than that of intermediate and central row atoms, because of spin imbalance due to low coordination.
The spin density distribution is symmetric in the direction for parallelogram, rectangular and centered hexagonal structures.
As the number of rows in the parallelogram Nws increase, the negative spin density in the interstitial region gradually increases from the center of the Nw to the terminal row. As discussed in Sec. (III.3.1), this leads to reduced magnetic moment in PR-4 structure in comparison with RT-4 structure, which exhibits negative spin densities only on the terminal row atoms.

#### iii.3.2 Magnetic anistropy energy

Besides a qualitative understanding of the changes in the magnetic moments as the number of rows is increased, we are interested in knowing the preferred spin orientations in these nanowires from an applications perspective. At reduced dimensions, the asymmetry in the structure has a significant contribution to the shape anisotropy along with the magnetocrystalline anisotropy. The magnetic shape anisotropy was determined from the classical magnetic dipole interaction between the magnetic moments in the system. Figure 4 shows the magnetic dipolar interaction energy along the Cartesian axes. One dimensional linear nanowire has the lowest energy when the magnetic moments are aligned along the wire directions. The magnetic moments along the perpendicular direction to the wire plane are unstable, as the dipolar energy is positive. This is in agreement with earlier work.Tung and Guo (2007) The magnetic dipolar energy of the medium axis reduces with increasing number of rows in the nanowires, but is still higher than that of the easy axis of rotation. All nanowires have the hard axis aligned perpendicular to the wire plane and the magnetic dipolar energy of the hard axis increases as the number of rows in the nanowires are increased.

The magnetic shape anisotropy for Ni NW’s is shown in Fig. 5. The shape anisotropy energy decreases sharply from linear wire to two row nanowires by 0.006 meV/atom. Further increase in the number of rows, gradually decreases the anisotropy energy. The MSA energy decreases from linear nanowire to double row rectangular/parallelogram structure, however, for higher number of rows, the value of MSA is enhanced. This indicates that, as the nanostrip becomes thicker, the magnetic moments are unlikely to orient in the direction due to an increase in the shape anisotropy energy.

The magnetic anisotropy energy (MAE) has another contribution from magnetocrystalline anisotropy (MCA), which originates from the spin orbit coupling in the system. Our calculations show that, the MCA energy is about 200 times larger than the shape anisotropy energy, and hence has a strong impact on the total magnetic anisotropy energy. MCA for parallelogram and rectangular Nws is plotted in Fig. 6 . It is interesting to see that for parallelogram structures is found to decrease as the number of rows is increased in the Nw. However, for rectangular structures, reduces from RT-1 to RT-2 Nw, but, further increase in the number of rows increases the MCA. This behavior of magneto-crystalline anisotropy energy is qualitatively similar to that of the net magnetization (Fig. 3), as the number of rows is increased. for parallelogram and rectangular nanowires has a higher MCA than of respective nanowires, implying it is energetically expensive to have magnetic moments directed in vacuum along the direction. As the number of rows (i.e., thickness) of the parallelogram Nws increase, the energy required to rotate the easy magnetization axis is reduced and converges to 0.1 meV/atom for the (111) film. For (100) film, due to rotational invariance at 90 in the film plane, we observe that the axial magnetization is isotropic in the XY-plane (==0.9 meV/atom). However, the hard axis remains perpendicular to the plane.

The total magnetic anisotropy energy (MAE) is plotted in Fig. 7. The MAE ( and ) is dominated mainly by and values. The linear nanowires prefer to magnetize along the wire axis, in agreement with earlier results.Tung and Guo (2007); Navas et al. (2008) However, our result for PR-1 Nw is in contradiction with the reported resultsTung and Guo (2007) as we observe that the easy axis of magnetization points along the wire direction and not perpendicular to the wire direction. Our calculations show that, in rectangular and parallelogram nanowires, the easy axis is along the wire direction, except for the magic structure “RT-2”, where, the easy axis is perpendicular to the wire direction and in the geometrical -plane of the structure. We mention that, in case of RT-2 structure, although the magnetic dipolar energy shows the preferred magnetization along the wire direction, the energy due to interaction between spin and orbital motion of electrons has a much stronger contribution in the MAE, which leads to the magnetization axis being perpendicular to the wire axis.

In general, we observe that the axial MAE, is always larger than , in all the nanowires. Thus, the external energy required to rotate the magnetization axis perpendicular to the plane is much higher than the energy required
to rotate in the plane but perpendicular to the wire axis.

Rows | Linear Nw | Parallelogram Nws | Rectangular Nws | |||

in Nws | A | B | A | B | A | B |

1 | 14 | 14 | - | - | - | - |

2 | - | - | 0 | 0 | 0 | 0 |

3 | - | - | -25 | -25 | 17 | 0 |

4 | - | - | 9 | 29 | 0 | 0 |

5 | - | - | 0 | 27 | 19 | 19 |

6 | - | - | 0 | 13 | 9 | 9 |

#### iii.3.3 Ballistic anisotropic magnetoresistance (BAMR)

The MAE also has a significant effect on the ballistic transport in the nanostrips. The ballistic conductance is influenced by spin orbit coupling and exhibits anisotropy with the magnetization direction.Sokolov et al. (2007) There is a change in the ballistic conductance when the magnetization direction changes with respect to the current direction as the number of bands crossing the Fermi level changes due to the spin orbit coupling interaction.Velev et al. (2005) We have investigated the size dependence of in parallelogram and rectangular nanostrips with increasing number of rows. We have calculated the when the magnetization direction is parallel to and parallel to and list these results in Table-4. Our result on in linear wire is in agreement with the results of Sokolov et al.Sokolov et al. (2007) and Velev et al.Velev et al. (2005) In addition, we find that for the magnetization direction M and M , the number of conduction channels are identical, thus giving the same ratio in both the cases. In general, the Ni nanostrips exhibit a nonlinear behavior in with increasing widths. The nanostrips exhibit finite size fluctuations in . The double row structures exhibit no change in conductance with change in magnetization directions. PR-2 is the only structure with a negative . In rectangular NWs, the with M and M are identical except for the RT-2 structure, which has zero with M . In rectangular Nws, the magnetization direction does not affect the conductance properties as strongly as in the parallelogram shaped wires, where the ratio is sensitive to the in plane and out of plane perpendicular orientation of the magnetization field.

#### iii.3.4 Stoner’s criterion in Ni Nws

The magnetism in 3 transition metals such as Ni and Co is explained on the basis of theory of itinerant electrons.Stoner (1938); Slater (1936) Our spin DFT results for Ni Nws have the ferromagnetic ground states to be lower in energy than antiferromagnetic and non magnetic states.

We have analyzed the appearance of magnetic ground state using Stoner’s model.Stoner (1938); Zeller (2006); Marcus and Moruzzi (1988); Stollhoff et al. (1990) The product is plotted for Ni Nws, monolayer films (Ni (111) and Ni (100)) in Fig. 8 and the values of the exchange splitting and normalized DOS are listed in Table-5 for comparison. The dotted horizontal line in Fig. 8 shows the product , which is the demarking value for ferromagnetic behavior. The value of the product depends on the Stoner integral which is derived from the exchange splitting in the ferromagnetic (or antiferromagnetic) system. It has been shown that, the Stoner parameter () does not depend on the atomic arrangement in the system.Zeller (2006) However it can be seen from Table-5, the Stoner parameter is sensitive to the dimensions of the system. In general, the Stoner parameter for rectangular nanowires exhibits larger values than that of the parallelogram nanowires, when compared for the respective number of rows. The value of for (111) and (100) monolayer film is small than that of the bulk Ni (). Our calculation of the Stoner criterion in bulk Ni is in agreement with the previous results.Christensen et al. (1988)

The coupling between the first nearest neighbors in infinite Ni atomic chain () indicates that, the noncollinear magnetic alignment is not stable,Tung and Guo (2011) however in small finite zigzag Ni chains, noncollinear magnetic ground states have been observed.Ataca et al. (2008) Our spin spiral relativistic calculations are in agreement with the results on infinite chains. The strong magnetic anisostropy energy in comparison with the exchange splitting energy enforces the magnetic moments in the infinite Ni nanowires to orient in ferromagnetic order.

iThe least stable linear Nw has the product larger than all parallelogram nanowires including Ni (111) monolayer and Ni bulk. Among rectangular Nws, RT-3 Nw exhibits the largest value of the product (2.75).‘:w The value of is a measure of strength of ferromagnetism in system. With an increase in the number of rows in (111) direction, the strength merely decreases with an increase in the number of rows upto 4, however it shows irregular nature for number of rows . The monolayer film shows indicating clear ferromagnetic nature and is in agreement with the previous results.Freeman et al. (1982); Wu and Freeman (1999) As the number of rows are increased in (100) direction, the shows a dip at RT-1 structure and a maximum at RT-3 Nw. The product decreases with an increase in the number of rows. However, similar to (111) oriented structures, all rectangular nanowires exhibit ferromagnetic behavior along with Ni (100) monolayer.

Existence of magnetically dead layers of Ni when deposited on non-magnetic substrates viz., Cu, Al and Pd has been described earlier,Liebermann et al. (1970); Pierce and Siegmann (1974); Bergmann (1978); Meservey et al. (1980); Gradmann (1977); Freeman et al. (1982); Jarlborg and Freeman (1980) when the number of atomic layers is less than 3 or 4. However, our calculations for freestanding monolayers show that, the systems retains ferromagnetism when not interacting with any substrate. This result points out the role of hybridization of the nonmagnetic substrate atoms in contact with the film/slabs. The previous results show that, in case of pure Ni surfaces, magnetically dead layers are not observed, however, the surface layers show enhanced magnetic moments.Erskine (1980); Wang and Freeman (1980); Eberhardt et al. (1980) In analogy with this, our results for Ni nanowires demonstrate that, the 2D Ni Nws exhibit enhanced magnetic moments than that of bulk, and show an absence of dead layers.

The ferromagnetic strength calculated from Stoner’s criterion (Table- 5) is larger for Ni Nws in comparison with the bulk Ni. In addition, as discussed in Sec. (III.3.1), the magnetic moments in Ni Nws are enhanced than that of bulk. These two properties can be correlated with the enhanced magnetic anisotropy energy (III.3.2) for Ni Nws in comparison with the bulk. The large magnetic anisotropy energy in Ni Nws in comparison with the bulk, forces the magnetic moments to couple ferromagnetically and requires high energy to fluctuate /decouple the neighboring magnetic moments from the stable ferromagnetic alignment. This is in agreement with the Mermin-Wagner’s theorem, that 2D Ni Nws can show ferromagnetic ground state, because these Nws do not show isotropic Heisenberg interaction, instead they show very large energy differences for different orientations of the magnetic moments.

System | I () | |||
---|---|---|---|---|

LR | 0.966 | 0.84 | 3.11 | 2.60 |

PR-1 | 0.680 | 0.72 | 3.27 | 2.37 |

PR-2 | 0.828 | 0.96 | 1.93 | 1.85 |

PR-3 | 0.673 | 0.78 | 2.00 | 1.55 |

PR-4 | 0.761 | 0.89 | 2.25 | 2.00 |

PR-5 | 0.704 | 0.82 | 2.14 | 1.75 |

RT-1 | 0.920 | 1.02 | 1.98 | 2.02 |

RT-2 | 0.686 | 1.07 | 2.40 | 2.58 |

RT-3 | 0.925 | 1.12 | 2.46 | 2.75 |

RT-4 | 0.901 | 1.05 | 2.09 | 2.19 |

RT-5 | 0.870 | 0.98 | 2.14 | 2.09 |

Ni(111) ML | 0.695 | 0.89 | 1.59 | 1.40 |

Ni(100) ML | 0.775 | 0.92 | 2.02 | 1.87 |

Bulk | 0.635 | 1.01 | 1.91 | 1.91 |

## Iv Conclusion

We have performed systematic investigations on infinite length, nickel nanowire structures of increasing widths. Our investigations show that the parallelogram structure is the most stable Nw geometry. Rectangular Nws have a lower stability in comparison with structures that incorporate parallelogram motifs in their geometry. The stability of the parallelogram motif is due to the increased coordination of atoms and due to contributions from electrons. In a particular geometrical structure, Nws of higher widths have a higher stability. Our studies on the conductance behavior of the Ni Nws show that more stable structures have a lower conductance as compared to the less stable structures. All rectangular nanowires have higher spin dependent conductance than the stable parallelogram nanowires. In any geometry, the number of spin down conductance channels is more than the spin up conductance channels and the number of spin down conduction channels increases substantially with increasing widths of the Nws.

The parallelogram and rectangular Nws have different magnetic behaviors with increasing widths. Except for the RT-2 structure, the magnetic moments of the Nws are enhanced as compared with the bulk and single layered (111) and (100) films. While magnetization decreases with small fluctuations in parallelogram Nws towards their (111) monolayer limit, in rectangular Nws, it initially decreases with RT-2 having the smallest magnetic moment and then increases. RT-2 exhibits a magnetic anomaly with a smaller magnetic moment in comparison with all other higher coordination rectangular NWs as well as Ni (100) monolayer. This behavior is contrary to the observation that magnetic moments decrease as the coordination of atoms increases. It is not clear from the small widths investigated here, how the magnetic moments in rectangular wires converge to their (100) monolayer value and further investigations are required to understand this.

The decrease in magnetization values in parallelogram Nws is on account of the negative polarization of and orbitals, that decreases the spin imbalance due to electrons. In rectangular Nws, the RT-2 is the only wire that has small negative and polarization, as compared to all other rectangular wires which exhibit only negative polarization. The magnetic anisotropy energy is lower than in all the Nws. The MAE decreases with increasing width of parallelogram nanowires, and for rectangular nanowires MAE increases with increasing widths. The easy axis of magnetization is found to be along the periodic direction of the wire, except for RT-2 structure, where it is perpendicular. RT-2 Nw exhibits an anomalous behavior in all magnetic aspects as compared with the other rectangular Nws and hence it is a magic structure. The ratio has a non-linear behavior with increasing widths and is sensitive to the magnetization orientation in parallelogram shaped nanostrips.

All the nickel nanowires investigated exhibit a ferromagnetic behavior based on the Stoner criterion including (111) and (100) monolayer. We see that the exchange splitting depends significantly on the geometrical structure of the nanowire. The rectangular shaped nanowires exhibit enhanced Stoner exchange parameter than those of parallelogram nanowires. The RT-3 structure exhibits the highest Stoner product amongst all Nws investigated.

## V Acknowledgments

The computational work was carried out using B.A.R.C. mainframe supercomputers (Ameya, Ajeya and Adhya clusters), Yuva-PARAM at C-DAC Pune and the high performance computing facility at the Centre for Modeling and Simulation at the Savitribai Phule Pune University. The authors thank Rudolf Zeller for fruitful discussions. V. K. acknowledges B.A.R.C. for research fellowship during the course of this work, Institut für Festkörperforschung (IFF), Forschungszentrum-Jülich and DST-DAAD program for local hospitality and travel support. V. S. would like to acknowledge the Dept. of Science and Technology (DST), BCUD-Savitribai Phule Pune University and the DST-DAAD program for funding support. Y. M. acknowledges support from HGF-YiG program VH-NG-513.

## References

- Tung and Guo (2007) J. C. Tung and G. Y. Guo, Phys. Rev. B 76, 094413 (2007).
- Skomski (2008) R. Skomski, Simple Models of Magnetism (Oxford University Press, 2008), ISBN 978-0-19-857075-2.
- Doll (2003) K. Doll, Surface Science 544, 103 (2003), ISSN 0039-6028.
- Smogunov et al. (2003a) A. Smogunov, A. D. Corso, and E. Tosatti, Surface Science 532-535, 549 (2003a), ISSN 0039-6028, proceedings of the 7th International Conference on Nanometer-Scale Science and Technology and the 21st European Conference on Surface Science.
- Krutzen and Springelkamp (1989) B. C. H. Krutzen and F. Springelkamp, Journal of Physics: Condensed Matter 1, 8369 (1989).
- Brookes et al. (1992) N. B. Brookes, A. Clarke, and P. D. Johnson, Phys. Rev. B 46, 237 (1992).
- Borgiel and Nolting (1990) W. Borgiel and W. Nolting, Zeitschrift fÃ¼r Physik B Condensed Matter 78, 241 (1990), ISSN 0722-3277, 10.1007/BF01307842.
- Zarechnaya et al. (2008) E. Zarechnaya, N. Skorodumova, S. Simak, B. Johansson, and E. Isaev, Computational Materials Science 43, 522 (2008), ISSN 0927-0256.
- Wimmer et al. (1984) E. Wimmer, A. J. Freeman, and H. Krakauer, Phys. Rev. B 30, 3113 (1984).
- Freeman et al. (1982) A. J. Freeman, D.-S. Wang, and H. Krakauer, Journal of Applied Physics 53, 1997 (1982), ISSN 0021-8979.
- Freeman and Wu (1991) A. Freeman and R.-Q. Wu, Journal of Magnetism and Magnetic Materials 100, 497 (1991), ISSN 0304-8853.
- Bennett and Cooper (1971) A. J. Bennett and B. R. Cooper, Phys. Rev. B 3, 1642 (1971).
- Takayama et al. (1976) H. Takayama, K.-P. Bohnen, and P. Fulde, Phys. Rev. B 14, 2287 (1976).
- Krakauer et al. (1983) H. Krakauer, A. J. Freeman, and E. Wimmer, Phys. Rev. B 28, 610 (1983).
- Jepsen et al. (1982) O. Jepsen, J. Madsen, and O. K. Andersen, Phys. Rev. B 26, 2790 (1982).
- Zhu and Hermanson (1983) X.-Y. Zhu and J. Hermanson, Phys. Rev. B 27, 2092 (1983).
- Tersoff and Falicov (1982) J. Tersoff and L. M. Falicov, Phys. Rev. B 26, 6186 (1982).
- Li et al. (1990) Y. Li, M. Farle, and K. Baberschke, Phys. Rev. B 41, 9596 (1990).
- Pick and Dreyssé (1992) i. c. v. Pick and H. Dreyssé, Phys. Rev. B 46, 5802 (1992).
- Gay and Richter (1986) J. G. Gay and R. Richter, Phys. Rev. Lett. 56, 2728 (1986).
- Zelený et al. (2009) M. Zelený, M. Šob, and J. Hafner, Phys. Rev. B 79, 134421 (2009).
- Sabirianov (2006) R. Sabirianov, Journal of Magnetism and Magnetic Materials 300, 136 (2006), ISSN 0304-8853, the third Moscow International Symposium on Magnetism 2005.
- Smogunov et al. (2004a) A. Smogunov, A. D. Corso, and E. Tosatti, Surface Science 566-568, 390 (2004a), ISSN 0039-6028, proceedings of the 22nd European Conference on Surface Science.
- Smogunov et al. (2002) A. Smogunov, A. D. Corso, and E. Tosatti, Surface Science 507-510, 609 (2002), ISSN 0039-6028.
- Ooka et al. (2001) Y. Ooka, T. Ono, and H. Miyajima, Journal of Magnetism and Magnetic Materials 226-230, 1848 (2001), ISSN 0304-8853, proceedings of the International Conference on Magnetism (ICM 2000).
- Wernsdorfer et al. (2005) W. Wernsdorfer, R. Clérac, C. Coulon, L. Lecren, and H. Miyasaka, Phys. Rev. Lett. 95, 237203 (2005).
- Ataca et al. (2008) C. Ataca, S. Cahangirov, E. Durgun, Y.-R. Jang, and S. Ciraci, Phys. Rev. B 77, 214413 (2008).
- Mermin and Wagner (1966) N. D. Mermin and H. Wagner, Phys. Rev. Lett. 17, 1133 (1966).
- Smogunov et al. (2004b) A. Smogunov, A. Dal Corso, and E. Tosatti, Phys. Rev. B 70, 045417 (2004b).
- Sirvent et al. (1996) C. Sirvent, J. G. Rodrigo, S. Vieira, L. Jurczyszyn, N. Mingo, and F. Flores, Phys. Rev. B 53, 16086 (1996).
- Li et al. (2007) H. Li, X. Q. Zhang, F. W. Sun, Y. F. Li, K. M. Liew, and X. Q. He, Journal of Applied Physics 102, 013702 (pages 4) (2007).
- García-Mochales et al. (2005) P. García-Mochales, S. Peláez, P. Serena, E. Medina, and A. Hasmy, Applied Physics A: Materials Science and Processing 81, 1545 (2005), ISSN 0947-8396, 10.1007/s00339-005-3393-z.
- García-Mochales et al. (2008) P. García-Mochales, R. Paredes, S. Peláez, and P. A. Serena, Nanotechnology 19, 225704 (2008).
- Velev et al. (2005) J. Velev, R. F. Sabirianov, S. S. Jaswal, and E. Y. Tsymbal, Phys. Rev. Lett. 94, 127203 (2005).
- Kresse and Hafner (1993) G. Kresse and J. Hafner, Phys. Rev. B 47, 558 (1993).
- Kresse and Furthmüller (1996a) G. Kresse and J. Furthmüller, Phys. Rev. B 54, 11169 (1996a).
- Kresse and Furthmüller (1996b) G. Kresse and J. Furthmüller, Comp. Mater. Sci. 6, 15 (1996b).
- Kresse and Joubert (1999) G. Kresse and D. Joubert, Phys. Rev. B 59, 1758 (1999).
- Perdew et al. (1992) J. P. Perdew, J. A. Chevary, S. H. Vosko, K. A. Jackson, M. R. Pederson, D. J. Singh, and C. Fiolhais, Phys. Rev. B 46, 6671 (1992).
- Kashid et al. (2011) V. Kashid, V. Shah, and H. Salunke, Journal of Nanoparticle Research 13, 5225 (2011), ISSN 1388-0764, 10.1007/s11051-011-0507-8.
- Imry and Landauer (1999) Y. Imry and R. Landauer, Rev. Mod. Phys. 71, S306 (1999).
- Oetzel et al. (2008) B. Oetzel, M. Preuss, F. Ortmann, K. Hannewald, and F. Bachstedt, Phys. Stat. Sol. B 245, 854 (2008).
- Treske et al. (2010) U. Treske, F. Ortmann, B. Oetzel, K. Hannewald, and F. Bechstedt, Phys. Status Solidi A 207, 304 (2010).
- Wen et al. (2005) Y.-H. Wen, Z.-Z. Zhu, G.-F. Shao, and R.-Z. Zhu, Physica E: Low-dimensional Systems and Nanostructures 27, 113 (2005), ISSN 1386-9477.
- Smogunov et al. (2003b) A. Smogunov, A. D. Corso, and E. Tosatti, Surface Science 532-535, 549 (2003b), ISSN 0039-6028, proceedings of the 7th International Conference on Nanometer-Scale Science and Technology and the 21st European Conference on Surface Science.
- Bergmann (1978) G. Bergmann, Phys. Rev. Lett. 41, 264 (1978).
- Pourovskii et al. (1999) L. Pourovskii, N. Skorodumova, Y. K. Vekilov, B. Johansson, and I. Abrikosov, Surf. Sci. 439, 111 (1999).
- Dal Corso and de Gironcoli (2000) A. Dal Corso and S. de Gironcoli, Phys. Rev. B 62, 273 (2000).
- Liebermann et al. (1970) L. Liebermann, J. Clinton, D. M. Edwards, and J. Mathon, Phys. Rev. Lett. 25, 232 (1970).
- Navas et al. (2008) D. Navas, K. R. Pirota, P. M. Zelis, D. Velazquez, C. A. Ross, and M. Vazquez, Journal of Applied Physics 103, 07D523 (pages 3) (2008).
- Sellmyer et al. (2001) D. J. Sellmyer, M. Zheng, and R. Skomski, Journal of Physics: Condensed Matter 13, R433 (2001).
- Whitney et al. (1993) T. M. Whitney, P. C. Searson, J. S. Jiang, and C. L. Chien, Science 261, 1316 (1993), eprint http://www.sciencemag.org/content/261/5126/1316.full.pdf, URL http://www.sciencemag.org/content/261/5126/1316.abstract.
- Nielsch et al. (2001) K. Nielsch, R. B. Wehrspohn, J. Barthel, J. Kirschner, U. Gösele, S. F. Fischer, and H. Kronmüller, Applied Physics Letters 79, 1360 (2001), ISSN 0003-6951.
- Sokolov et al. (2007) A. Sokolov, C. Zhang, E. Y. Tsymbal, J. Redepenning, and B. Doudin, Nat. Nano. 2, 171 (2007).
- Stoner (1938) E. C. Stoner, Proc. R. Soc. A 165, 372 (1938).
- Slater (1936) J. C. Slater, Phys. Rev. 49, 537 (1936).
- Zeller (2006) R. Zeller, Computational Nanoscience: Do It Yourself!, vol. 31 (John von Neumann Institute for Computing, Jülich, NIC Series, 2006), ISBN 3-00-017350-1.
- Marcus and Moruzzi (1988) P. M. Marcus and V. L. Moruzzi, Phys. Rev. B 38, 6949 (1988).
- Stollhoff et al. (1990) G. Stollhoff, A. M. Oleś, and V. Heine, Phys. Rev. B 41, 7028 (1990).
- Christensen et al. (1988) N. Christensen, O. Gunnarsson, O. Jepsen, and O. Andersen, Le Journal de Physique Colloques 49, C8 (1988).
- Tung and Guo (2011) J. C. Tung and G. Y. Guo, Phys. Rev. B 83, 144403 (2011).
- Wu and Freeman (1999) R. Wu and A. Freeman, Journal of Magnetism and Magnetic Materials 200, 498 (1999), ISSN 0304-8853.
- Pierce and Siegmann (1974) D. T. Pierce and H. C. Siegmann, Phys. Rev. B 9, 4035 (1974).
- Meservey et al. (1980) R. Meservey, P. Tedrow, and V. Kalvey, Solid State Communications 36, 969 (1980), ISSN 0038-1098.
- Gradmann (1977) U. Gradmann, Journal of Magnetism and Magnetic Materials 6, 173 (1977), ISSN 0304-8853.
- Jarlborg and Freeman (1980) T. Jarlborg and A. J. Freeman, Phys. Rev. Lett. 45, 653 (1980).
- Erskine (1980) J. L. Erskine, Phys. Rev. Lett. 45, 1446 (1980).
- Wang and Freeman (1980) C. S. Wang and A. J. Freeman, Phys. Rev. B 21, 4585 (1980).
- Eberhardt et al. (1980) W. Eberhardt, E. W. Plummer, K. Horn, and J. Erskine, Phys. Rev. Lett. 45, 273 (1980), URL http://link.aps.org/doi/10.1103/PhysRevLett.45.273.