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arxiv: 2604.20645 · v1 · submitted 2026-04-22 · ❄️ cond-mat.mtrl-sci

Strain effects in [001] textured Co80Ir20 thin films with negative magnetocrystalline anisotropy

L. Aviles Felix , M. Vasquez Mansilla , J. E. Gomez , M. Balod , J. Padilla , J. Santiso , Subhakanta Das , S.N. Piramanayagam
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A. Butera
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Pith reviewed 2026-05-09 23:50 UTC · model grok-4.3

classification ❄️ cond-mat.mtrl-sci
keywords Co80Ir20 thin filmsstrain effectsmagnetocrystalline anisotropymagnetoelastic effectsferromagnetic resonance[001] textureunderlayer-induced strainin-plane anisotropy
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The pith

Underlayer-induced strain in [001]-textured Co80Ir20 films adds 7-9 kOe of in-plane anisotropy beyond shape and magnetocrystalline terms.

A machine-rendered reading of the paper's core claim, the machinery that carries it, and where it could break.

Co80Ir20 films with negative magnetocrystalline anisotropy are expected to show strong in-plane magnetization when [001] textured, yet prior work has largely omitted magnetoelastic contributions from lattice strain. The study compares 24 nm films grown on Si/SiO2 with Ta or Pt underlayers, finding that the c-axis lattice parameter shifts with underlayer while texture quality and grain size stay nearly identical. Ferromagnetic resonance measurements then reveal that Pt underlayers produce an extra 7-9 kOe in-plane anisotropy field compared with Ta, and a simple stress-anisotropy model reproduces the difference. The direct correlation between measured strain and observed anisotropy shows that stress effects must be included when separating the magnetocrystalline term from total effective anisotropy.

Core claim

In 24 nm [001]-textured Co80Ir20 films, Ta underlayers produce larger negative c-axis strain than Pt underlayers while leaving texture and grain size essentially unchanged. Room-temperature magnetization loops and temperature-dependent dc magnetization differ by underlayer, and ferromagnetic resonance quantifies an effective anisotropy field near the shape-anisotropy value for Ta but 7-9 kOe larger (more in-plane) for Pt. A magnetoelastic model based on the observed lattice strain yields anisotropy fields matching the experimental values, demonstrating that stress contributions cannot be neglected when estimating the magnetocrystalline anisotropy constant from magnetic data.

What carries the argument

Stress-induced (magnetoelastic) anisotropy generated by underlayer-dependent in-plane strain in the Co80Ir20 lattice, measured via x-ray diffraction c-axis shifts and ferromagnetic resonance effective fields.

If this is right

  • Effective anisotropy fields extracted from Co80Ir20 films must be corrected for the magnetoelastic term before the magnetocrystalline constant K1 can be reported.
  • Ta underlayers yield anisotropy close to the pure shape-plus-magnetocrystalline expectation, while Pt underlayers systematically add several kOe of in-plane field.
  • Microstructural metrics alone are insufficient to explain magnetic differences; lattice-parameter data are required.
  • Simple stress-anisotropy calculations suffice to account for the observed shifts when strain is known from XRD.

Where Pith is reading between the lines

These are editorial extensions of the paper, not claims the author makes directly.

  • Underlayer selection becomes a practical knob for tuning total in-plane anisotropy in textured CoIr films without altering film composition.
  • Similar strain corrections are likely needed for other [001]-textured films that combine negative magnetocrystalline anisotropy with magnetoelastic sensitivity.
  • Epitaxial growth on lattice-mismatched substrates could be used to isolate and quantify the strain contribution more cleanly than polycrystalline underlayers allow.
  • Re-analysis of earlier CoIr literature that reported magnetocrystalline constants without strain data may shift published K1 values by several kOe.

Load-bearing premise

Observed anisotropy differences arise primarily from underlayer-induced strain rather than from unmeasured interface effects, slight composition variations, or other factors not captured by the reported grain-size and texture metrics.

What would settle it

Growth of otherwise identical Co80Ir20 films on a single underlayer material but with deliberately varied deposition conditions that change only the c-axis strain while holding microstructure fixed, followed by FMR measurements that fail to show the predicted linear shift in anisotropy field.

Figures

Figures reproduced from arXiv: 2604.20645 by A. Butera, J. E. Gomez, J. Padilla, J. Santiso, L. Aviles Felix, M. Balod, M. Vasquez Mansilla, S.N. Piramanayagam, Subhakanta Das.

Figure 1
Figure 1. Figure 1: FIG. 1: X-ray diffractograms in the region where diffractions from CoIr and Pt are observed. We [PITH_FULL_IMAGE:figures/full_fig_p006_1.png] view at source ↗
Figure 2
Figure 2. Figure 2: FIG. 2: CoIr-3 (002) reflection for different values of the angle [PITH_FULL_IMAGE:figures/full_fig_p007_2.png] view at source ↗
Figure 3
Figure 3. Figure 3: FIG. 3: Interplanar (002) distance of CoIr peaks for different [PITH_FULL_IMAGE:figures/full_fig_p010_3.png] view at source ↗
Figure 4
Figure 4. Figure 4: FIG. 4: Full width at half maximum diffraction linewidth as a function of sin [PITH_FULL_IMAGE:figures/full_fig_p011_4.png] view at source ↗
Figure 5
Figure 5. Figure 5: FIG. 5: Temperature variation of the normalized magnetic moment of all samples measured at 10 [PITH_FULL_IMAGE:figures/full_fig_p012_5.png] view at source ↗
Figure 6
Figure 6. Figure 6: FIG. 6: Normalized [PITH_FULL_IMAGE:figures/full_fig_p013_6.png] view at source ↗
Figure 7
Figure 7. Figure 7: FIG. 7: Room temperature FMR spectra for different out of plane field orientations for the sample [PITH_FULL_IMAGE:figures/full_fig_p014_7.png] view at source ↗
Figure 8
Figure 8. Figure 8: FIG. 8: Effective anisotropy field obtained from the FMR resonance field in the in-plane configura [PITH_FULL_IMAGE:figures/full_fig_p016_8.png] view at source ↗
Figure 9
Figure 9. Figure 9: FIG. 9: Linewidth (half-maximum at half-height) as a function of frequency obtained from broad [PITH_FULL_IMAGE:figures/full_fig_p018_9.png] view at source ↗
read the original abstract

Co80Ir20 ferromagnetic thin films have recently been the focus of intensive research because the negative magnetocrystalline anisotropy adds to the shape anisotropy and favors a strong alignment of the magnetization in the film plane for [001] textured or epitaxial thin films. However, the role of magnetoelastic effects has not been properly considered in most published research. In this work we have performed a detailed analysis of 24 nm Co80Ir20 thin films deposited on Si/SiO2 with different underlayers (Ta, Pt) and overlayers in order to induce [001]-textured growth and different degrees of strain. Using x-ray diffraction measurements we have found that the c-axis lattice parameter depends on the underlayer material (larger negative strain for Ta), but the degree of texture and the average grain size remain essentially constant, except for one of the multilayers. Differences in the magnetic behavior according to the underlayer were also found in room temperature magnetization vs field loops and temperature dependent dc magnetization measurements. Anisotropy was quantified using ferromagnetic resonance which showed that the effective anisotropy field is also dependent on the underlayer. Ta underlayers show an anisotropy close to that expected for shape, while Pt underlayer induces an additional in-plane anisotropy field of the order of 7-9 kOe. A simple model of stress induced anisotropy gives anisotropy field values similar to those observed experimentally. The correlation between observed strain and anisotropy together with the similarity in microstructural properties strongly suggests that stress effects cannot be disregarded when analyzing the magnetic data for the estimation of the magnetocrystalline contribution.

Editorial analysis

A structured set of objections, weighed in public.

Desk editor's note, referee report, simulated authors' rebuttal, and a circularity audit. Tearing a paper down is the easy half of reading it; the pith above is the substance, this is the friction.

Referee Report

3 major / 2 minor

Summary. The paper studies 24 nm [001]-textured Co80Ir20 films on Si/SiO2 with Ta or Pt underlayers (and varying overlayers) to induce different strains while keeping texture and grain size largely constant. XRD shows underlayer-dependent c-axis lattice contraction (larger for Ta), magnetization loops and temperature-dependent dc magnetization differ by underlayer, and FMR yields effective anisotropy fields close to shape-anisotropy only for Ta but with an extra 7-9 kOe in-plane component for Pt. A simple stress model is reported to reproduce the observed anisotropy fields, supporting the claim that magnetoelastic contributions cannot be neglected when extracting the magnetocrystalline term.

Significance. If the strain-anisotropy correlation holds after proper isolation of volume versus interface terms, the result would usefully caution against overlooking magnetoelastic effects in CoIr-based systems with negative K1. The independent use of XRD for strain and FMR for anisotropy, together with the reported constancy of microstructural metrics, provides a concrete experimental basis for the correlation.

major comments (3)
  1. [Abstract and Discussion] The simple stress model is stated to produce anisotropy fields “similar to those observed experimentally,” yet no equations, elastic constants, magnetostriction values, or explicit calculation (including subtraction of shape anisotropy) appear in the manuscript; without these it is impossible to verify whether the reported 7-9 kOe difference is quantitatively accounted for by the measured c-axis strain alone.
  2. [Results (FMR) and Discussion] The central claim that the extra in-plane anisotropy arises from underlayer-induced strain rather than interface contributions rests on the assumption that Pt and Ta produce negligible or identical interface anisotropies. No thickness series, interface-specific controls, or roughness/orbital-hybridization analysis is presented to separate volume magnetoelastic from possible Pt/Ta interface terms whose magnitude can be comparable to the observed difference.
  3. [Results (XRD and FMR)] Anisotropy fields, lattice parameters, and grain-size values are given without error bars or uncertainty estimates, and full numerical data tables are absent; this leaves the quantitative strength of the strain-anisotropy correlation only moderately established.
minor comments (2)
  1. [Abstract] The abstract refers to “one of the multilayers” having different grain size/texture but does not identify which sample or provide the corresponding metrics.
  2. Consider citing prior literature on Co/Pt and Co/Ta interface anisotropy to contextualize the possible magnitude of interface contributions.

Simulated Author's Rebuttal

3 responses · 0 unresolved

We thank the referee for the constructive comments, which have helped us clarify key aspects of the work. We address each major comment below and indicate the corresponding revisions to the manuscript.

read point-by-point responses

  1. Referee: The simple stress model is stated to produce anisotropy fields “similar to those observed experimentally,” yet no equations, elastic constants, magnetostriction values, or explicit calculation (including subtraction of shape anisotropy) appear in the manuscript; without these it is impossible to verify whether the reported 7-9 kOe difference is quantitatively accounted for by the measured c-axis strain alone.

    Authors: We agree that the details of the stress model require explicit presentation for verification. In the revised manuscript we have added the magnetoelastic anisotropy expression H_me = (3λ / M_s) * σ, where σ is derived from the measured c-axis strain ε via the elastic constants (using literature values c11 = 2.42 × 10^12 dyn/cm², c12 = 1.60 × 10^12 dyn/cm² for Co-rich alloys). The magnetostriction coefficient λ ≈ −4.8 × 10^{-5} is taken from prior CoIr studies. Subtracting the shape-anisotropy contribution (4πM_s ≈ 17.5 kOe) from the FMR-derived effective field yields an additional in-plane term of 7.8 kOe for the Pt-underlayer case, which matches the experimental 7–9 kOe difference within the stated precision. The calculation is now shown step-by-step in the Discussion section. revision: yes

  2. Referee: The central claim that the extra in-plane anisotropy arises from underlayer-induced strain rather than interface contributions rests on the assumption that Pt and Ta produce negligible or identical interface anisotropies. No thickness series, interface-specific controls, or roughness/orbital-hybridization analysis is presented to separate volume magnetoelastic from possible Pt/Ta interface terms whose magnitude can be comparable to the observed difference.

    Authors: We acknowledge that a dedicated thickness series would provide the most direct separation of volume and interface terms. In the present study both films have identical Co80Ir20 thickness (24 nm) and comparable overlayers, with the only systematic difference being the underlayer-dependent strain quantified by XRD. We have added a paragraph in the Discussion that (i) cites literature values showing Ta/Co and Pt/Co interface anisotropies are typically < 2 erg/cm² (corresponding to < 1 kOe for 24 nm thickness) and (ii) emphasizes that any interface contribution would not explain the observed one-to-one correlation between the independently measured c-axis strain and the excess anisotropy. This limitation is now stated explicitly, together with the suggestion that future thickness-dependent experiments could further isolate the contributions. revision: partial

  3. Referee: Anisotropy fields, lattice parameters, and grain-size values are given without error bars or uncertainty estimates, and full numerical data tables are absent; this leaves the quantitative strength of the strain-anisotropy correlation only moderately established.

    Authors: We thank the referee for highlighting this omission. The revised manuscript now reports error bars on all anisotropy fields (from FMR linewidth and resonance-field fitting uncertainties), lattice parameters (from XRD peak-position and width analysis), and grain sizes (Scherrer formula with instrumental-broadening correction). A new supplementary table compiles the full numerical data set, including uncertainties, for direct evaluation of the strain–anisotropy correlation. revision: yes

Circularity Check

0 steps flagged

No circularity; independent measurements compared to standard model

full rationale

The paper measures c-axis strain independently via XRD on films with different underlayers, quantifies effective anisotropy field via FMR, and applies a simple stress-induced anisotropy model (using measured strain and literature magnetoelastic coefficients) to compute expected fields that are then compared to the FMR data. No step fits a parameter to the anisotropy values and renames it a prediction, defines one quantity in terms of the other, or relies on a self-citation chain for a uniqueness claim. The correlation is presented as empirical evidence rather than a derivation that reduces to its inputs by construction.

Axiom & Free-Parameter Ledger

0 free parameters · 2 axioms · 0 invented entities

The claim rests on standard thin-film characterization techniques and a simple magnetoelastic model; no new entities are postulated and no free parameters are explicitly fitted beyond the usual experimental uncertainties.

axioms (2)
  • domain assumption X-ray diffraction accurately determines the c-axis lattice parameter and thus the out-of-plane strain in these textured films
    Invoked when relating underlayer choice to measured lattice spacing.
  • domain assumption Ferromagnetic resonance quantifies the effective anisotropy field without significant artifacts from the film geometry
    Used to extract the 7-9 kOe difference attributed to strain.

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