Research and design of modern magnetic materials frequently require a microscopic understanding of the structure and properties of the system, [1][2][3] which can be challenging to determine with macroscale measurements. [4][5][6] On the other hand, advanced magnetic imaging, such as magnetic transmission x-ray microscopy (MTXM), [7][8][9][10][11][12] Lorentz transmission electron microscopy, 13 spinpolarized scanning tunneling microscopy, 14,15 spin-polarized low energy electron microscopy (SPLEEM), 16,17 photoemission electron microscopy, 18,19 and scanning electron microscopy with polarization analysis, [20][21][22] can provide critical visualization of real-space magnetic configurations. However, magnetic imaging over local areas faces limitations in effectively and quantitatively resolving the sometimes large variations in material properties of a system. An ideal research technique would bridge these two domains: quantitative macroscale measurements with exemplary spatial resolution or microscopy that can quantitatively survey magnetic property variations. 6 The first-order reversal curve (FORC) technique has shown promise as a bridge of the former type. 9,[23][24][25][26][27][28] This technique analyzes the evolution of the magnetization along a series of partial hysteresis loops-macroscopic measurements-to extract magnetic characteristics such as microscopic interaction fields and intrinsic coercivity distributions. These properties are often not associated with any particular regions of the sample but represent sample-scale ensemble-averaged distributions. Furthermore, FORC distributions have been extensively used to provide insights into the magnetization reversal processes, 9,[29][30][31][32][33][34][35][36][37][38] yet direct confirmation with magnetic imaging, particularly one carried out using the same magnetic field cycling protocol, has been lacking. In fact, performing FORC measurements with microscopy, which is sensitive to magnetic structure, provides a mechanism to extract quantitative insights from microscopic probes, becoming a bridge of the latter type.
In this work, we combine the FORC technique with MTXM to quantitatively evaluate magnetization reversal behavior. [26][27][28]39,40 Combining these two techniques allows the magnetic interaction fields and intrinsic coercivity distributions to be quantitatively extracted from local areas. MTXM further provides the ability to highlight specific regions or phases 3 using its element-specific, high-resolution 11 imaging capability. The MTXM-FORCs measured on a CoTb film with perpendicular anisotropy are directly compared to FORCs measured on the same sample with alternating gradient magnetometry (AGM). Since the FORC technique has been proposed as a macroscopic measurement, which can "fingerprint" microscopic reversal behavior, 9,[29][30][31][32][33][34][35][36][37][38]41 comparing FORC measurements captured with macroscopic techniques and microscopy presents an ideal opportunity to confirm this capability. 42,43 The results of this work lay the foundation for broader applications of FORC and MTXM, including applying the FORC technique to exceedingly small samples to quantitatively extract microscopic information, as demonstrated on a single permalloy (Py) microstructure with vortex-like flux-closure structures.
In the first sample, a single magnetic film of Pt(5 nm)/ CoTb(20 nm)/Pt(5 nm) with perpendicular magnetic anisotropy (PMA) was grown by sputtering on an x-ray transparent amorphous Si 3 N 4 (200 nm) membrane in a 5 mTorr Ar atmosphere in an ultrahigh vacuum sputtering chamber. The Pt layers were used as an adhesion/seed layer and a capping layer, respectively. MTXM images were obtained in the out-of-plane geometry on the XM-1 microscope (BL 6.1.2) at the Advanced Light Source using 778 eV x rays, probing the Co L 3 edge. 7 Fresnel zone-plate optics were used for x-ray focusing and imaging, and the full field images were recorded by an x-ray sensitive CCD camera. Magnetic contrast was obtained using the XMCD effect at the Co L 3 edge. The use of XMCD makes this technique inherently element-specific. For the present CoTb system, which consist of only a single magnetic phase, the element specific sensitivity does not provide an additional insight, but it can be used to separate the magnetic signals in a system with more than one magnetic material or phase. To obtain FORC data, XMCD images were recorded at each magnetic field step following the FORC sequence described below. From the images, the areas of the black and white contrasted domains, A White and A Black , were measured, corresponding to the positive and negative out-of-plane directions, respectively. A normalized magnetization is defined as MMic = A White -A Black A White +A Black . Magnetometry measurements were performed at room temperature using an alternating gradient magnetometer (AGM). The magnetization from the AGM is identified by the variable M.
In the second sample, a single 40 nm thick, rectangular (3 × 2 μm 2 ) microstructure of permalloy (Ni 80 Fe 20 ) with in-plane magnetization was prepared on a Si 3 N 4 window using electronbeam lithography and liftoff techniques. For this size and shape of microstructure, the magnetization curls into a pair of vortex structures, e.g., Landau patterns, with opposite circularities; circularity is defined as the direction of the in-plane winding of the vortex structures and can be clockwise or counter-clockwise. 22,44 MTXM images were obtained using circularly polarized 708 eV x rays, probing the Fe L 3 edge. 8,34 Imaging was performed in a tilted geometry, with the x rays impinging at 30 ○ relative to the sample normal, capturing the in-plane component of the magnetization. The black and white contrasts indicate regions with magnetization parallel and antiparallel to the positive magnetic field direction, respectively. The magnetic sensitivity was enhanced by subtracting images taken with left-and right-circularly polarized x-rays. The magnetization from a single microstructure is calculated to be 180 pemu, which is beyond the sensitivity of conventional magnetometers.
First-order reversal curve measurements for both MTXM and AGM were performed following a previously reported magnetic field sequence. 9,26,45 From positive saturation, the applied magnetic field is reduced to a scheduled reversal field, HR. At HR, the field sweep direction is reversed and the magnetization, M or MMic., is measured as the applied field, H, is increased back to positive saturation. This process is repeated for HR between the positive and negative saturated states, thus measuring a family of FORCs. 9,31 A mixed second order derivative is applied to the dataset to extract the FORC distribution:
(increasing H at a constant HR), the derivative ∂(M or M Mic ) ∂H captures domain growth or "up-switching" events. The derivative ∂ ∂H R distinguishes new up-switching events on adjacent FORC branches. 26 It is thus important to note that the absence of any feature in the FORC diagram only indicates that the magnetization is changing at the same rate as that on adjacent FORCs (adjacent in HR).
The families of FORCs and the corresponding FORC distributions for the CoTb sample are shown in Fig. 1, measured by (a) and (b) AGM and (c) and (d) MTXM, respectively. FORC distributions from both techniques exhibit a boomerang feature, typical of PMA thin films that reverse by a domain nucleation and growth mechanism. 9,32 Along with decreasing HR, the horizontal ridge appears at μ 0 HR = -45 mT [highlighted as feature 1 in Fig. 1(b)] and corresponds to the initial nucleation and rapid propagation of reversed domains when the applied field is reduced from positive saturation. 8 As the field is increased from HR back to saturation, an elongated horizontal FORC feature emerges as the previously reversed domains return to positive saturation. The horizontal feature is accompanied, at more negative HR, by a pair of vertical negative/positive FORC features [marked as features 2 and 3 in Fig. 1 Together, these results confirm that FORCs measured by MTXM imaging, which probes the microscopic responses, are quantitatively comparable to FORC measurements performed by traditional magnetometry methods that capture the collective magnetic response from the entire sample. This agreement can be expected for measurements in which the field of view (in this case, the 10 μm diameter provided in the MTXM images) captures behavior that is representative of the system as a whole. This agreement illustrates that FORC measurements performed with conventional magnetometry also contain nanoscale details about the magnetization reversal.
To illustrate the step-by-step microscopic magnetization reversal process, Fig. 2 shows the family of FORCs measured with MTXM [Fig. 2(a)], the AGM FORC diagram [Fig. 2(b)] and a selection of the MTXM images from the CoTb film [Fig. 2(c)]. The AGM FORC diagram is used due to its higher resolution, while the MTXM family of FORCs is used because of its direct correspondence with the MTXM images, with each image in Fig. 2(c) marked by a star in Fig. 2(a). Following the FORC measurement sequence, the film was first saturated, then the field was reduced to an HR, and MTXM images were taken as the magnetic field was increased to saturation. Images taken on FORCs starting at μ 0 HR > -40 mT show no magnetic con-trast, indicating that the magnetization remains in the saturated state at HR; since M is constant in the saturated region, the derivative Thus, the vertical FORC features [labeled 2 and 3 in Fig. 2(b)] are directly confirmed to correspond to large regions of the sample becoming negatively saturated and re-nucleating domains along the FORC branch. Achieving negative saturation suppresses domain growth between H = HR and the rapid propagation event at μ 0 H = 38 mT, resulting in the negative FORC feature [labeled 2 in Fig. 2(b)]. Between μ 0 H = 38 and 55 mT, domain nucleation and rapid propagation occur, facilitating the positive FORC feature (labeled 3). At μ 0 H > 55 mT, the domain progression is largely independent of μ 0 HR and thus does not result in any appreciable feature in the FORC distribution.
Performing FORCs using MTXM provides a unique opportunity to capture the microscopic magnetic configurations, which are inaccessible with conventional magnetometry. These configurations are important because FORC captures the magnetic evolution from each reversal field, which is presumed to be evolved sequentially between neighboring HR. Without this sequential evolution, the initial configuration can contribute to the shape of each FORC branch, presenting a new variable in deciphering the FORC distribution. This ansatz is tested by comparing the magnetic configuration at each HR and subsequent evolution. Specifically, at μ 0 HR = -40 mT, there is a large, single negative domain [outlined in yellow dashes in Fig. 2(c)]; at μ 0 HR = -45 mT, this domain is partly reoriented back to positive (orange dashes); and at μ 0 HR = -50 mT, some of these regions are reoriented back to negative (blue dashes); meanwhile, other regions, which were negative at μ 0 HR = -45 mT have now become positive (orange dashes). This flip-flopping of the magnetization against the applied field is unlikely to be the result of sequential evolution, but rather a consequence of random thermal activation at the nucleation field and transient domain evolution. The resulting domain configurations are local energy minima that the FORC protocol is able to access as the energy landscape is changed during the field cycling. 46 The domain evolution from each of these states is also shown to be different [Fig. 2(c)], confirming the ansatz. However, the FORC diagrams for the conventional (whole sample) and microscopic FORCs were already shown to be very comparable, implying that the ensemble average accurately represents behavior down-to the scale of the MTXM field of view (80 μm 2 ), seemingly indifferent to the initial configuration at HR.
The above results confirm the interpretation of the "boomerang" FORC feature put forward by Davies et al. 41 and the negative FORC features presented by Gilbert et al. 26 These results also show that FORC measurements can be performed using microscopy-based techniques and show quantitative agreement with traditional collective magnetometry measurements. Microscopy FORCs present opportunities to perform quantitative measurements on exceedingly small magnetic elements. To demonstrate this, FORC measurements are performed on the aforementioned permalloy microstructure. The rectangular microstructure harbors two flux-closure Landau structures, analogous to a magnetic vortex, as shown in Fig. 3.
The family of MTXM FORCs and the FORC distribution for the single microstructure are shown in Figs. 3(a) and 3(b), respectively. The FORC distribution exhibits the two-lobe "butterfly" feature, similar to magnetometry FORC measurements taken on arrays of vortex-state nanodots. 31 Analogous to the mechanistic reconstruction of the FORC distribution performed above for the boomerang feature, or previously for the wishbone, 26 the reversal sequence of the vortex system, shown in Fig. 3(c), can be used to construct the butterfly feature. The top row of the MTXM images, showing the FORC, which starts at μ 0 HR = +40 mT, does not exhibit vortices but shows minor distortion of the magnetic configuration from the saturated state. Similar to the CoTb sample in saturation, the near-saturated state has ∂M ∂H ≈ 0 and contributes very little to the FORC distribution. At μ 0 HR = 7 mT the FORC branch shows a dramatic 90% reduction in the magnetization at the reversal field [Fig. 3(a)], signaling vortex nucleation, which is also observed in the MTXM images [second row in Fig. 3(c)]. As the field is increased from HR to positive saturation, the vortex moves transverse to the magnetic field and annihilates the top and bottom edges of the microstructure. Annihilation from opposite sides indicates that the vortices have opposite chirality, 47 as would be expected to minimize the exchange energy at their meeting point. As this FORC has ∂M ∂H > 0, while every FORC (μ 0 HR > 7 mT) has ∂M ∂H ≈ 0 , the second order derivative used to calculate the FORC distribution is non-zero, resulting in a positive feature in the FORC distribution, labeled feature 1 in Fig. 3(b). Next, the FORC branch measured at μ 0 HR = -40 mT is shown in the middle row of Fig. 3(c). The double vortices are now shown displaced from the centerline of the structure, and as the field is increased back towards positive saturation, they migrate across the structure, annihilating again at opposite edges of the microstructure. The migration of the vortex across the microstructure is shown to occur reversibly such that the magnetization is independent of HR, which in-turn implies the FORC distribution is zero. 31 The FORC branch at μ 0 HR = -60 mT shows the evolution of the vortex, moving further towards the edge with height. The evolution of the vortex from HR to positive saturation shows the vortex again moving across the microstructure. Comparing each field step in H to the prior FORCs (μ 0 HR = -40 and +7 mT) shows that the images are similar, again consistent with the reversible behavior of the vortex structure.
Next, the FORC branch μ 0 HR = -120 mT is considered. This HR is beyond the saturation field of the microstructure, as indicated by the first image. Increasing H toward positive saturation, ∂M ∂H ≈ 0, while the previous branch (μ 0 HR = -60 mT) ∂M ∂H > 0, implying the presence of a negative feature in the FORC distribution. While no such feature is observed here, likely due to the coarse field step, it has been observed previously in other vortex systems. 31,47 In this FORC distribution, a new positive feature is present at μ 0 H = -27 mT, indicating the re-nucleation of the vortices, also observed in the MTXM images. This re-nucleation event results in a positive feature in the FORC distribution, labeled feature 2. While feature 1 and feature 2, representing nominally symmetric events, should be the same magnitude, 31 in this case, feature 2 is blended with the negative feature due to the course field step, resulting in a visibly weaker feature. As H is increased towards positive saturation, the vortices reversibly migrate across the entire width of the microstructure and annihilate at the opposite edge from their nucleation. This annihilation generates one final feature in the FORC distribution, completing the "butterfly" FORC feature.
The butterfly-like FORC distribution for the vortex structure is a well-known example of a system with a large reversible component. 31,45,48 Capturing reversible features in the FORC distribution usually requires special analysis beyond the standard derivative since these features first appear on the boundary, H = HR. 40 In one approach, the data in this boundary region are treated separately, without the second order derivative. 48 Reversible magnetization is presumably independent of HR; thus, this is quite reasonable. Another approach is to extend the dataset, with a so-called constant extension being the most common. The constant extension is achieved by defining M(H < HR) ≡ M(HR), which is shown visually in Fig. 3(c) as the shaded regions to the left of the H = HR dashed line. The extended data were not measured but are simply a copy of the H = HR data. This approach quantitatively reproduces the reversible features. 45 With the extended dataset in-place, the images show a clear dependence in HR in the shaded regions, but no changes in H. Without changes in H, each extended region has ∂M ∂H = 0, and the ∂HR derivative between adjacent zeros is also zero, so no feature appears in the FORC distribution. The extended FORC dataset only manifests a feature at H = HR, at which point there are differences in both H and HR. Thus, the FORC distribution captures the nucleation and annihilation events in the parameter space (H > HR) and the reversible motion of the flux-closure structures at (H ≈ HR); the approximate symbol is used because the derivative is performed over the datapoints near the boundary, resulting in a smearing of the feature across the H = HR boundary.
In summary, microscopic magnetization reversal configurations in model systems of CoTb thin film and patterned permalloy elements have been studied by first-order reversal curve measurements using magnetic transmission x-ray microscopy. The FORC distribution calculated from the images quantitatively agreed with FORCs measured by conventional magnetometry, supporting the microscopic sensitivity of the FORC technique. By comparing the FORC distribution to the MTXM images, the physical origins of the boomerang-shaped feature in the CoTb film were directly confirmed. The ability to perform microscopic FORCs was demonstrated by measuring the reversal of a single Py microstructure with double vortices and calculating the FORC distribution, resulting in the expected butterfly-like FORC feature. Leveraging the element-specific, high spatial resolution characteristics of MTXM, and the quantitative insight from FORC measurements, the combined MTXM-FORC technique could provide new insights into studies of magnetic heterostructures and multi-component complex materials.
© Author(s) 2022
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