Publisher Correction: Small-angle neutron scattering modeling of spin disorder in nanoparticles

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Scientific REPORTS | 7:13060 | DOI: 10.1038/s41598-017-13457-2 where n is the number density of particles, ρ ∆ mag denotes the magnetic scattering-length density contrast between particle and matrix (essentially the difference in saturation magnetizations), V p is the particle volume, F(q) its form factor, and the α sin 2 factor is due to the dipolar nature of the neutron-magnetic interaction. For a single-domain particle, α denotes the angle between q and the magnetization M of the particle 38 . Figure 1 displays sketches of the two most common (perpendicular and parallel) SANS scattering geometries.
For many problems the macrospin model that is embodied in equation (1) is oversimplified, since it assumes homogeneous (or stepwise homogeneous) magnetization and, thus, ignores the complex spin structures that may appear at the nanoscale. As mentioned above, intraparticle spin disorder is due to the interplay between different magnetic interactions such as surface anisotropy and dipolar interaction, or to the presence of crystal defects. Therefore, SANS approaches based on the "standard model" [equation (1)] might be erroneous when the spatial dependence of the magnitude and direction of the magnetization M(r) is not taken into account 31 . Günther et al. 16 have suggested the presence of significant intraparticle spin disorder when analyzing SANS experiments on a Co nanorod array: the strong field dependence of Σ Ω d d / that these authors have observed could not be explained by the standard expression for Σ Ω d d / . Likewise, the polarized SANS experiments on ferromagnetic nanowires by Napolskii et al. 14 and by Maurer et al. 17 indicate that the nanowires' stray fields have to be taken into account in the magnetic form-factor derivation.
Micromagnetic computer simulations are ideally suited to tackle the above described problem, since one can include in a straightforward manner all the relevant inter-and intraparticle magnetic interactions (dipolar and Zeeman interactions, magnetic anisotropy, exchange), which in turn allows one to compute the magnetic SANS cross section for an inhomogeneously magnetized nanoparticle. Note that analytical micromagnetic calculations of the magnetic SANS cross section of nanoparticles are extremely difficult due to the nonlinear character of the underlying differential equations; a first attempt into this direction has been carried out by Metlov and Michels 34 , who computed the magnetic scattering related to vortices in thin submicron-sized soft ferromagnetic cylinders. Important aspects of computational micromagnetism are that (i) the parameter space can be relatively quickly scanned and that (ii) this methodology permits the investigation of the impact of the different interactions on magnetic SANS simply by switching on and off these interactions in simulations; such a procedure may then provide fundamental information on magnetic SANS. Up to now, however, this approach has only been used for studying bulk ferromagnets [39][40][41][42] , where not only the relevant magnetic interactions may strongly differ from those in nanoparticles, but where all phases (and not only the nanoparticle phase) comprising the material are ferromagnetic. Needless to say that for nanoparticles the particle shape also plays an important role for the spin configuration.
In this paper we employ micromagnetic computer simulations in order to investigate the magnetic SANS cross section of an isolated Co nanorod for different nanorod diameters. The choice of this particular system is motivated by the great interest from both the fundamental and technological point of view. Indeed, the structural and magnetic properties of elongated magnetic nanoobjects in the form of nanorods (or nanowires) have emerged as some of the most promising materials for functionalized magnetic nanostructures, with relevant interest in biomedicine 43 , permanent magnets 44 , and information technologies 4,45 . Cobalt nanowires may be suitable candidates Figure 1. Sketch of the perpendicular (a) and parallel (b) SANS scattering geometries. Note that the applied magnetic field H 0 is along e z in both geometries and that the angle θ describes the orientation of the scattering vector q on the two-dimensional detector. The average neutron wavelength λ is determined by the velocity selector; k 0 and k denote the wave vectors of the incident and the scattered neutrons; ψ 2 is the scattering angle, and ψ = = π λ q q sin 4 . In the small-angle approximation, the component of q along the incident beam is ignored.
for dense three-dimensional arrays of magnetic vortex-based media 9,46 and for the integration in nanooscillators based on arrays of magnetostatically coupled Co/Au segmented nanopillars; 47 in particular, synthesis improvements based on self-organization principles have made it possible to produce monocrystalline Co nanorods with controlled easy-axis orientations, which are frequently found to be almost perpendicular to the nanorod direction 46,48 . Depending on the orientation of the c-axis, the magnetization distribution at remanence can be tuned to be parallel to the nanowire axis, or to form a vortex structure when it is perpendicular. The paper is organized as follows: we begin the discussion with the saturated SANS cross sections, where the problem is a purely geometrical one. We then continue to discuss the magnetization distributions and the ensuing magnetic SANS in the remanent state as a function of the diameter-to-length ratio; here, strongly inhomogeneous magnetization structures determine the SANS cross sections of the nanorod. The decomposition of Σ Ω d d / M into the individual magnetization Fourier components in conjunction with computed hysteresis loops provides useful insights into the role of spin-misalignment scattering. The magnetic SANS cross sections for the two most often employed scattering geometries as well as information about the micromagnetic simulations can be found in the Methods section. We also refer the reader to the Supplemental Material, which contains many additional data.

Results and Discussion
In Fig. 2  are identical at saturation, except for a factor of 1/2 which comes in on azimuthally averaging equation (4). The results depicted in Fig. 2(a)-(c) confirm the expected behavior for which analytical results exist.
In the following we discuss the spin structures and related magnetic SANS cross sections in the remanent state as a function of the D/L ratio; the length of the nanorod is fixed at = L 500 nm and the diameter is varied between = D 30,60, and 90nm. As is well known, for such shape-anisotropic particles, the long-range magnetodipolar interaction gives rise to magnetic shape anisotropy, which tends to align the magnetic moments along the nanorod's long axis. On top of that, we consider an uniaxial magnetocrystalline anisotropy axis K u , which is directed along the cylinder's diameter (perpendicular to the long axis). As a consequence, the system behaves effectively like a biaxial magnetic material and the spin structure reflects the competition between both interactions; in particular, as D increases at constant L and at constant magnitude and direction of K u . Magnetization curves and spin structures for where the rod's long axis for both scattering geometries is parallel to the normal on the detector plane. For an inhomogeneously magnetized nanorod, the magnetization components M x y z , , depend explicitly on the position = x y z r { , , } and all three Fourier . It is seen in Fig. 2(d)-(e) that a more complicated SANS pattern than in the saturated state results (see detailed discussion below); we also note that although both Σ Ω d d / M are nearly identical, the corresponding magnetization curves (for H 0 perpendicular and parallel to the long axis) are quite different (compare Fig. 3(b) in the paper with Fig. 2(b) in the Supplemental Material). Importantly, the azimuthally-averaged data in Fig. 2(f) cannot be described anymore by the geometrical form-factor model [equations (1) and (2)], which assumes a uniform magnetization state. Away from saturation, the magnetic microstructure decomposes into several domains, which naturally have an average spatial extension that is smaller than the purely geometrical dimensions (L, D) of the nanorod. Therefore, the "form-factor" oscillations corresponding to these domains appear at larger values of the momentum transfer, as it becomes visible in Fig. 2(f). Note that in the following we restrict our considerations to the case of ⊥ k H 0 0 , which is the most often employed scattering geometry in magnetic SANS experiments.
Before we discuss in more detail the magnetic scattering cross sections of the nanowire, we would like to show in Fig. 3 some results for the hysteresis curves and internal spin structures at remanence; note that the applied field in Fig. 3  is reduced starting from saturation, the magnetization will rotate towards the shape-anisotropy axis. At remanence, the magnetization is then predominantly oriented along the x-direction, with some minor spin misalignment along the z-direction at the nanowire's end faces, and a vanishingly small magnetization component along the y-direction. The localized spin inhomogeneities at the end faces are related to the combined effects of the inhomogeneous dipole field of the rod, which tends to align the moments parallel to the surface of the nanorod's ends, the exchange interaction, which tries to keep the ferromagnetic order, and the magnetocrystalline anisotropy, which prefers the magnetization along the ±z-direction. In the center part of the = D 30 nm nanorod, the magnetic state at remanence is quite similar to the case without magnetocrystalline anisotropy (see Fig. 1(a) and upper left part in Fig. 3 in the Supplemental Material); the main changes between the hysteresis loops with and without magnetocrystalline anisotropy are the reduction of the field that is needed to saturate the system along the z-direction and the existence of a small coercivity. We will see below that as D increases (at constant L and K u ), the (reduced) dipolar interaction favors more complex magnetic structures such as domain wall or vortex states, which minimize the magnetic flux through the surface of the system.
Based on these (real-space) observations, the corresponding (reciprocal-space) SANS cross section and the magnetization Fourier components for the = D 30 nm nanorod (upper row in Fig. 4) can be understood:  theory for the Fourier components and in view of the facts that (i) the shape of the domains is field-dependent and not spherical (no single size parameter) and (ii) there exist no sharp boundaries between domains, the detailed analysis of the field dependence of the Fourier components and their relation to the real-space magnetization distribution is beyond the scope of this paper.
As mentioned above, increasing the nanorod's diameter results in the emergence of a variety of magnetization switching processes and complex inhomogeneous states, in agreement with results by other authors [48][49][50][51] ; this is in contrast to the case of vanishing magnetocrystalline anisotropy (see Figs. 1 and 3 in the Supplemental Material). While for = D 30 nm the shape anisotropy determines the magnetic configuration at remanence [ Fig. 3(a)], changing the diameter to = D 60 nm ( = . D L / 012) [ Fig. 3(b)] reduces the strength of the shape anisotropy and the competition with the magnetocrystalline anisotropy leads to a change in the switching mechanism from essentially coherent rotation to the nucleation and propagation of a transversal domain wall. The domain oriented along the x-direction grows by propagating a transversal domain wall at the lateral boundaries of the cylinder [compare inset in Fig. 3(b)]. Therefore, the remanent state is characterized by this transversal domain wall. The related SANS cross section (middle row in Fig. 4) can be seen as a combination of all three magnetization Fourier components; note also that the CT term is now increased in magnitude as compared to the = D 30 nm case (due to an increased ∼ M y contribution). Notably, the circular symmetry of the magnetic SANS cross section observed at remanence for the smallest diameter has now turned into a (slightly) vertically elongated pattern due to the existence of magnetization components perpendicular to the rod's axis, which directly result from the tranversal domain-wall configuration.
Finally, when the diameter is increased to = D 90 nm corresponding to an aspect ratio of = . D L / 018 [ Fig. 3(c)], there is again a change in the mechanism from the nucleation and propagation of transversal domain-wall-like structures to vortex-like configurations. Indeed, the spin texture which stabilizes the system at remanence is a combination of different vortices (in those structures the magnetization is confined in the x-z-plane) with their cores aligned parallel and antiparallel to the y-direction, in other words, the vortex cores are oriented perpendicular to the plane that is spanned by the uniaxial and shape-anisotropy axes. As an example, Fig. 6 shows the spin distribution of the = D 90 nm nanorod. Consequently, the | | ∼ M y 2 Fourier component is small in magnitude and the SANS cross section (lower row in Fig. 4) is dominated by | | ∼ M x 2 and | | ∼ M z 2 , resulting in a distorted pattern with a slight elongation along the field direction. By comparison of the magnetization Fourier components along the rod (x) and the magnetocrystalline (z) axes, it can be seen that the shape anisotropy still contributes to the effective anisotropy, however, its strength is lowered as compared to the anisotropy created parallel to the rod's diameter, i.e., increasing the diameter reinforces the effect of the magnetocrystalline anisotropy. The CT term contributes to Σ Ω only with a low signal, which is related to the small volume fraction of vortex cores (small ∼ M y contribution, compare middle image in Fig. 6). Interestingly, at the smallest q, the CT term has inverted its sign compared to the = D 30 nm and = D 60 nm results, which may reflect an asymmetry of the magnetic configuration. In monocrystalline hcp Co nanowire arrays with = . D L / 0225, Ivanov et al. 9,46 have demonstrated that, at remanence, the magnetic structure can be composed of multiple stable magnetic vortex domains with different chirality.
The data for the individual Fourier components in Fig. 4 also reveal that these functions may explicitly depend on the angle θ in the detector plane. For bulk ferromagnets, it has been demonstrated by means of micromagnetic simulations that such an angular anisotropy is related to the magnetodipolar interaction [39][40][41][42] . We emphasize that the possible θ-dependency of the Fourier components adds on top of the trigonometric functions in the magnetic SANS cross sections [equations (4) and (5)], which are due to the dipolar nature of the neutron-magnetic matter interaction.
In order to grasp the deviation between the standard model [equation (1)] and the spin-misalignment SANS into one single parameter, we introduce the function  Figure 7 shows the results for η H ( ) 0 obtained by computing Σ Ω d d / M of the Co nanorod for both scattering geometries and for several H 0 -values between positive and negative saturation with and without magnetocrystalline anisotropy. For the computation of η, the average intensity at the respective characteristic q-value of π = ⁎ q D 2 / was used. The behavior of η H ( ) 0 for a uniformly magnetized shape-anisotropic nanoparticle [cf. the discussion regarding equation (1)] and for the two scattering geometries can be understood within the context of the Stoner-Wohlfarth model 52 : for k H 0 0 (corresponding to the case that the rod's long axis is parallel to H 0 ), the magnetization curve exhibits the well-known rectangular shape, implying that M points always along the z-direction; there is, of course, a switching from the +z to the −z direction at the nucleation field, but this feature appears to be too "sharp" to be resolved with the SANS technique. As a consequence, the scattering vector q is always perpendicular to M, so that the expectation value of the α sin 2 factor in equation (1) equals unity and the function η H ( ) 0 does not depend on the field; the corresponding scattering pattern is isotropic. For ⊥ k H 0 0 (corresponding to the case that the rod's long axis is perpendicular to H 0 ), the Stoner-Wohlfarth model predicts a linear paramagnetic-like decrease from saturation (along the horizontal z-direction) to a zero remanent magnetization, where now (due to the shape anisotropy) the magnetization points along the wire axis (x-direction). The expectation value of α sin 2 changes from a value of 1/2 at saturation to a value of 1 at  Fig. 7(c)]; here, the = D 90 nm rod exhibts a variation which is much smaller than the one of the = D 60 nm cylinder. This observation indicates that the magnitude of the spin-misalignment scattering of nanorods depends sensitively on their domain structure, which is determined by the nanoparticle's geometry (ratio D/L) and by the magnetic interactions, including the applied-field direction (compare also the Fourier images in Fig. 4). All in all, the results depicted in Fig. 7 reveal-for not too small nanoparticles-significant deviations from the standard model due to internal spin disorder. In order to account for these inhomogeneous spin structures and to understand the associated complex scattering patterns, micromagnetic simulations provide the key tool set for progressing the understanding of magnetic SANS on nanoparticles.

Conclusion and Outlook
We have presented the results of micromagnetic simulations of the magnetic microstructure and the ensuing magnetic small-angle neutron scattering (SANS) cross section of a single Co nanorod with a length of = L 500 nm and diameters of = D 30, 60 and 90 nm. This methodology has allowed us to unravel the intrinsic  Fig. 3(c)]. The wavy-like modulation of the nanorods's shape is an artifact related to representation of the spatial dependence of the magnetization vector field via arrows. denotes the angle between q and H 0 , whereas θ θ ≅ q q(cos , sin , 0) for k H 0 0 , where θ is measured between q and e x . These expressions demonstrate that SANS mainly probes correlations in the plane normal to k 0 . The applied field H 0 defines the z-axis of a Cartesian laboratory coordinate system for both geometries. Since the focus of this study is on magnetic (spin-misalignment) scattering, we have ignored the nuclear SANS contribution, which for a homogeneous particle can be described by the particle form factor. The magnetization Fourier amplitudes depend on the size and shape of the particle, but most importantly on the magnetic interactions determining the nanoparticle's spin structure. Using computer simulations based on the continuum theory of micromagnetics it becomes possible to include all the relevant intraparticle magnetic interactions such as magnetic anisotropy, magnetostatics, and exchange interaction. For a saturated nanoparticle, expressions (4) and (5) reduce to equations of the form of equation (1). With the aid of polarized neutrons it becomes possible to access nuclear-magnetic interference terms as well as purely chiral magnetic contributions.

Micromagnetic simulations.
We have performed micromagnetic simulations using the GPU-based open-source software package MuMax3 54 , which can calculate the space and time-dependent magnetic microstructure of nano-and micron-sized ferromagnets. Mumax3 employs a finite-difference discretization scheme of space using a two-dimensional or three-dimensional grid of orthorhombic cells. In the micromagnetic simulations we have taken into account all four standard contributions to the total magnetic Gibbs free energy: energy in the external magnetic field  Z , magnetodipolar interaction energy D  , energy of the (uniaxial) magnetocrystalline anisotropy ani  , and isotropic and symmetric exchange energy ex  : is the magnetostatic field, K u is the (first-order) uniaxial anisotropy constant, u is a unit vector indicating the anisotropy-axis direction, A is the exchange-stiffness constant, µ 0 denotes the permeability of free space, and the integrals are taken over the volume of the nanorod. The nanorod is represented as a cylinder with a fixed length of = L 500 nm, but with different diameters D (30, 60, and 90 nm); these dimensions are typical of real materials [12][13][14][15][16][17] . The magnetic materials parameters were set to the ones corresponding to bulk hcp Co 55  . Correspondingly, a cubic cell with a side length of 2 nm was used in order to discretize the nanorod. The K u -axis orientation with respect to the nanorods's long axis was chosen in-plane along the nanorod's diameter ( = ± u {0,0, 1} for ⊥ k H 0 0 and = ± u { 1,0,0} for k H 0 0 ), in agreement with experimental observations which report a strong crystal anisotropy with an easy axis oriented nearly perpendicular to the axis of the wire (e.g., ref. 56 ). The hysteresis loops were calculated as follows: the magnetic system was initially completely saturated by aligning the magnetic moments of all the computational cells along the z-axis. Then, the applied field was reduced in steps of 5 mT and the equilibrium magnetization state at each H 0 (and therefore the static spin configuration) was found by two equivalent methods; we employed both the "Relax" and "Minimize" functions of Mumax3, where the former solves the Landau-Lifshitz-Gilbert equation without the precessional term and the latter uses the conjugate-gradient method to find the configuration of minimum energy. The translational invariance of the grid obtained with the finite-difference method enables the usage of the Fast Fourier transformation technique for the computation of the Fourier components of the magnetization. We have used the FFTW library 57 to compute and analyze the Fourier components of our nanoscopic magnetic configurations. Thermal fluctuations were not taken into account in the simulations.