Abstract
We report the properties of first synthesized ceramic samples of a perovskite solid solution (PbFe1/2Ta1/2O3)x[(PbMg1/3Nb2/3O3)0.7(PbTiO3)0.3]1−x, x = 0.4, 0.5. The solution is a single-phase material contrary to broadly studied multiphase (magnetic/ferroelectric) composites. Both compounds are ferroelectrics with a diffuse phase transition. An increase in x value results in a decrease in phase transition diffuseness, and an increase in the remnant polarization. 207Pb NMR shows that iron ions are nonuniformly distributed over octahedral sites and tend to random occupation of these sites in the perovskite structure. In particular, the NMR data indicate a tendency to form regions with a higher concentration of iron in the perovskite structure. Magnetic measurements show the coexistence of superparamagnetic and paramagnetic phases in the samples. The paramagnetoelectric (PME) coefficients determined by a dynamic method at room temperature have values β ≈ 0.15 × 10−15 s A−1 (x = 0.4) and 0.54 × 10−15 s A−1 (x = 0.5) at low magnetic fields (± 300 Oe), which are three thousands times larger than that in most single-phase magnetoelectric materials. Our measurements show that the main contribution to the PME response is caused by the superparamagnetic phase. Because the ME response is proportional to dM2/dH, it can be amplified by many orders of magnitude for the multiferroics with the superparamagnetic phase due to a sharp change of magnetization with the field.
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References
Spaldin NA, Ramesh R (2008) Electric-field control of magnetism in complex oxide thin films. MRS Bull 33:1047–1050
Scott JF (2012) Applications of magnetoelectrics. J Mater Chem 22:4567–4574
Pyatakov AP, Zvezdin AK (2012) Magnetoelectric and multiferroic media. Physics Uspekhi 55:557–581
Cherifi RO, Ivanovskaya V, Phillips LC, Zobelli A, Infante IC, Jacquet E, Garcia V, Fusil S, Briddon PR, Guiblin N, Mougin A, Ünal AA, Kronast F, Valencia S, Dkhil B, Barthélémy A, Bibes M (2014) Electric-field control of magnetic order above room temperature. Nat Mater 13:345–351
Scott JF (2013) Room-temperature multiferroic magnetoelectrics. NPG Asia Mater 5(11):e72
Feibig M (2005) Revival of the magnetoelectric effect. J Phys D Appl Phys 38:R123–R152
Ryu J, Priya S, Uchino K, Kim H-E (2002) Magnetoelectric effect in composites of magnetostrictive and piezoelectric materials. J Electroceram 8:107–119
Smolenskii G, Loffe VA (1958) Communication No 71. Colloque International du Magnetisme, Grenoble
Bokov V, Myl’nikova I, Smolenskii GA (1962) Ferroelectric antiferromagnetics. Sov Phys JETP 15:447–449
Sanchez DA, Ortega N, Kumar A, Roque-Malherbe R, Polanco R, Scott JF, Katiyar RS (2011) Symmetries and multiferroic properties of novel room-temperature magnetoelectrics: lead iron tantalate–lead zirconate titanate (PFT/PZT). AIP Adv 1:042169
Martin LW, Ramesh R (2012) Multiferroic and magnetoelectric heterostructures. Acta Mater 60:2449–2470
Evans DM, Schilling A, Kumar A, Sanchez D, Ortega N, Arredondo M, Katiyar RS, Gregg JM, Scott JF (2013) Magnetic switching of ferroelectric domains at room temperature in multiferroic PZTFT. Nat Commun 4:1534
Sanchez DA, Ortega N, Kumar A, Sreenivasulu G, Katiyar RS, Scott JF, Evans DM, Arredondo-Arechavala M, Schilling A, Gregg JM (2013) Room-temperature single phase multiferroic magnetoelectrics: Pb(Fe, M)x(Zr, Ti)(1–x)O3 [M = Ta, Nb]. J Appl Phys 113:074105
Evans DM, Schilling A, Kumar A, Sanchez D, Ortega N, Katiyar RS, Scott JF, Gregg JM (2014) Switching ferroelectric domain configurations using both electric and magnetic fields in Pb(Zr, Ti)O3–Pb(Fe, Ta)O3 single-crystal lamellae. Philos Trans R Soc A 372:20120450
Schiemer J, Carpenter MA, Evans DM, Gregg JM, Schilling A, Arredondo M, Alexe M, Sanchez D, Ortega N, Katiyar RS, Echizen M, Colliver E, Dutton S, Scott JF (2014) Studies of the room-temperature multiferroic Pb(Fe0.5Ta0.5)0.4(Zr0.53Ti0.47)0.6O3: resonant ultrasound spectroscopy, dielectric, and magnetic phenomena. Adv Funct Mater 24:2993–3002
Schiemer JA, Lascu I, Harrison RJ et al (2016) Elastic and anelastic relaxation behaviour of perovskite multiferroics I: PbZr0.53Ti0.47O3 (PZT)–PbFe0.5Nb0.5O3 (PFN). J Mater Sci 51:10727–10760. https://doi.org/10.1007/s10853-016-0280-2
Schiemer JA, Lascu I, Harrison RJ et al (2017) Elastic and anelastic relaxation behaviour of perovskite multiferroics II: PbZr0.53Ti0.47O3 (PZT)–PbFe0.5Ta0.5O3 (PFT). J Mater Sci 52:285–304. https://doi.org/10.1007/s10853-016-0330-9
Glinchuk MD, Eliseev EA, Morozovska AN (2014) Novel room temperature multiferroics on the base of single-phase nanostructured perovskites. J Appl Phys 116:054101
Glinchuk MD, Eliseev EA, Morozovska AN (2016) Landau–Ginzburg description of anomalous properties of novel room temperature multiferroics Pb(Fe1/2Ta1/2)x(Zr0.53Ti0.47)1−xO3 and Pb(Fe1/2Nb1/2)x(Zr0.53Ti0.47)1−xO3. J Appl Phys 119:024102
Kuzian RO, Laguta VV, Richter J (2014) Lieb–Mattis ferrimagnetic superstructure and superparamagnetism in Fe-based double perovskite multiferroics. Phys Rev B 90:134415
Kuzian RO, Richter J, Kuz’min MD, Hayn R (2016) Lieb–Mattis ferrimagnetism in magnetic semiconductors. Phys Rev B 93:214433
Laguta VV, Stephanovich VA, Savinov M et al (2014) Superspin glass phase and hierarchy of interactions in multiferroic PbFe1/2Sb1/2O3: an analog of ferroelectric relaxors? New J Phys 16:113041
Coey JMD, Douvalis AP, Fitzgerald CB, Venkatesan M (2004) Ferromagnetism in Fe-doped SnO2 thin films. Appl Phys Lett 84:1332–1334
Hou SL, Bloembergen N (1965) Paramagnetoelectric effects in NiSO4·6H2O. Phys Rev 138:A1218–A1226
Laguta VV, Morozovska AN, Eliseev EA, Raevski IP, Raevskaya SI, Sitalo EI, Prosandeev SA, Bellaiche L (2016) Room-temperature paramagnetoelectric effectin magnetoelectric multiferroics Pb(Fe1/2Nb1/2)O3 and its solid solution with PbTiO3. J Mater Sci 51:5330–5342. https://doi.org/10.1007/s10853-016-9836-4
Laguta VV, Stephanovich VA, Raevski IP, Raevskaya SI, Titov VV, Smotrakov VG, Eremkin VV (2017) Magnetoelectric effect in antiferromagnetic multiferroic Pb(Fe1/2Nb1/2)O3 and its solid solutions with PbTiO3. Phys Rev B 95:014207
Falqui A, Lampis N, Geddo-Lehmann A, Pinna G (2005) Low-temperature magnetic behavior of perovskite compounds PbFe1/2Ta1/2O3 and PbFe1/2Nb1/2O3. J Phys Chem 109:22967–22970
Choudhury RNP, Rodriguez C, Bhattacharya P, Katiyar RS, Rinaldi C (2007) Low-frequency dielectric dispersion and magnetic properties of La, Gd modified Pb(Fe1/2Ta1/2)O3 multiferroics. J Magn Magn Mater 313:253–260
Bharti C, Dutta A, Shannigrahi S, Sinha TP (2012) Electronic structure, magnetic and electrical properties of multiferroic PbFe1/2Ta1/2O3. J Magn Magn Mater 324:955–960
Lampis N, Franchini C, Satta G, Geddo-Lehmann A, Massidda S (2004) Electronic structure of PbFe1/2Ta1/2O3: crystallographic ordering and magnetic properties. Phys Rev B 69:064412
Zhu WZ, Kholkin A, Mantas PQ, Baptista JL (2000) Preparation and characterisation of Pb(Fe1/2Ta1/2)O3 relaxor ferroelectric. J Eur Ceram Soc 20:2029–2034
Choi SW, Shrout RTR, Jang SJ, Bhalla AS (1989) Dielectric and pyroelectric properties in the Pb(Mg1/3Nb2/3)O3–PbTiO3 system. Ferroelectrics 100(1):29–38
Feng Z, Zhao X, Luo H (2006) Composition and orientation dependence of dielectric and piezoelectric properties in poled Pb(Mg1/3Nb2/3)O3–PbTiO3 crystals. J Appl Phys 100:024104
Swartz SL, Shrout TR (1982) Fabrication of perovskite lead magnesium niobate. Mater Res Bull 17:1245–1250
Ernst R, Bodenhausen S, Wokaun A (1987) Principles of NMR in One and two dimensions. Oxford University Press, New York
Kumar MM, Srinivas A, Surynarayana SV, Kumar GS, Bhimasankaram T (1998) An experimental setup for dynamic measurement of magnetoelectric effect. Bull Mater Sci 21:251–255
Shvartsman VV, Kleemann W, Dec J, Xu ZK, Lu SG (2006) Diffuse phase transition in BaTi1−xSnxO3 ceramics: an intermediate state between ferroelectric and relaxor behavior. J Appl Phys 99:124111
Bogs M, Beige H, Pitzius P, Schmitt H (1992) Linear and nonlinear dielectric, elastic and electromechanical properties of Pb(Sc1/2Ta1/2)O3 ceramics. Ferroelectrics 126(1):197–202
Choi SW, Shrout TR, Jang SJ, Bhalla AS (1989) Morphotropic phase boundary in Pb(Mg1/3Nb2/3)O3–PbTiO3 system. Mater Lett 8(6–7):253–255
Geddo-Lehmann A, Sciau P (1999) Ferroelastic symmetry changes in the perovskite PbFe0.5Ta0.5O3. J Phys Condens Matter 11:1235–1245
Nomura S, Takabayashi H, Nakagawa T (1968) Dielectric and magnetic properties of Pb(Fe1/2Ta1/2)O3. Jpn J Appl Phys 7:600–604
Santos IA, Eiras JA (2001) Phenomenological description of the diffuse phase transition in ferroelectrics. J Phys Condens Matter 13:11733–11740
Zagorodniy YuO, Kuzian RO, Kondakova IV, Maryško M, Chlan V, Štěpánková H, Olekhnovich NM, Pushkarev AV, Radyush YuV, Raevski IP, Zalar B, Laguta VV, Stephanovich VA (2018) Chemical disorder and 207Pb hyperfine fields in the magnetoelectric multiferroic Pb(Fe1/2Sb1/2)O3 and its solid solution with Pb(Fe1/2Nb1/2)O3. Phys Rev Mater 2:014401
Kouřil K, Chlan V, Štĕpánková H, Řezníček R, Laguta VV, Raevski IP (2015) NMR study of multiferroic iron niobate perovskites. Acta Phys Pol A 127(2):234–236
Bedanta S, Kleemann W (2009) Supermagnetism. J Phys D Appl Phys 42:013001
Wiekhorst F, Shevchenko E, Weller H, Kötzler J (2003) Anisotropic superparamagnetism of monodispersive cobalt–platinum nanocrystals. Phys Rev B 67:224416
Opechowski W (1937) On the exchange interaction in magnetic crystals. Physica 4:181
Schmidt H-J, Lohmann A, Richter J (2011) Eighth-order high-temperature expansion for general Heisenberg Hamiltonians. Phys Rev B 84:104443
Lohmann A, Schmidt H-J, Richter J (2014) Tenth-order high-temperature expansion for the susceptibility and the specific heat of spin-Heisenberg models with arbitrary exchange patterns: application to pyrochlore and kagome magnets. Phys Rev B 89:014415
Raevski IP, Titov VV, Malitskaya MA et al (2014) Studies of ferroelectric and magnetic phase transitions in multiferroic PbFe0.5Ta0.5O3–PbTiO3 solid solution ceramics. J Mater Sci 49:6459–6466. https://doi.org/10.1007/s10853-014-8376-z
Raevski IP, Molokeev MS, Misyul SV et al (2015) Studies of ferroelectric and magnetic phase transitions in multiferroic PbFe0.5Ta0.5O3. Ferroelectrics 475(1):52–60
Cho SY, Kim JS, Jang MS (2006) Dielectric, ferroelectric and ferromagnetic properties of 0.8PbFe0.5Ta0.5O3–0.2PbTiO3 ceramics. J Electroceram 16:369–372
Nan CW, Bichurin MI, Dong S, Viehland D, Srinivasan G (2008) Multiferroic magnetoelectric composites: historical perspective, status, and future directions. J Appl Phys 103:031101
Laguta V, Rosa J, Jastrabik L, Blinc R, Cevc P, Zalar B, Remskar M, Raevskaya S, Raevski I (2010) 93Nb NMR and Fe3+ EPR study of local magnetic properties of magnetoelectric Pb(Fe1/2Nb1/2)O3. Mater Res Bull 45:1720–1727
Battle PD, Gibb T, Herod A, Kim S-H, Munns P (1995) Investigation of magnetic frustration in A2FeMO6 (A = Ca, Sr, Ba; M = Nb, Ta, Sb) by magnetometry and Mössbauer spectroscopy. J Mater Chem 5:865–870
Battle PD, Gibb T, Herod A, Hodges J (1995) Sol–gel synthesis of the magnetically frustrated oxides Sr2FeSbO6 and SrLaFeSnO6. J Mater Chem 5:75–78
Blinc R, Laguta VV, Zalar B, Zupancic B, Itoh M (2008) O17 and 93Nb NMR investigation of magnetoelectric effect in Pb(Fe1/2Nb1/2)O3. J Appl Phys 104:084105
Kuzian RO, Kondakova IV, Dare AM, Laguta VV (2014) Magnetic interactions in disordered perovskite PbFe1/2Nb1/2O3 and related compounds: dominance of nearest-neighbor interaction. Phys Rev B 89:024402
Raevski IP, Kubrin SP, Raevskaya SI, Sarychev DA, Prosandeev SA, Malitskaya MA (2012) Magnetic properties of PbFe1/2Nb1/2O3: Mössbauer spectroscopy and first-principles calculations. Phys Rev B 85:224412
Diaz S, Suárez N, Faloh J, Sánchez J, Leccabue F et al (1997) Magnetic properties of PbFe12O19 hexaferrites powders obtained by metallorganic decomposition. Le Journal de Physique IV 07(C1):C1-333–C1-334
Yang N, Yang H, Jia J, Pang X (2007) Formation and magnetic properties of nanosized PbFe12O19 particles synthesized by citrate precursor technique. J Alloys Compd 438:263–267
Chaudhury S, Rakshit SK, Parida SC et al (2008) Studies on structural and thermo-chemical behavior of MFe12O19(s) (M = Sr, Ba and Pb) prepared by citrate–nitrate gel combustion method. J Alloys Compd 455:25–30
Bezlepkin AA, Kuntsevich SP, Kostyukov VI (2015) Orientational and relaxation features of the dynamic magnetic susceptibility of PbFe12O19 upon transition from the magnetically ordered to paramagnetic state. Phys Solid State 57:2213–2216
Pullar RC (2012) Hexagonal ferrites: a review of the synthesis, properties and applications of hexaferrite ceramics. Prog Mater Sci 57:1191–1334
Albanese G, Díaz-Castañón S, Leccabue F, Watts BE (2000) Mössbauer and magnetic investigation of scandium and indium substituted PbFe12O19 hexagonal ferrite. J Mater Sci 35:4415–4420. https://doi.org/10.1023/A:1004869310024
Maryško M, Frait Z, Krupička S (1997) FMR and static magnetic properties of gallium substituted magnetoplumbite. J. Phys. IV (France) 7:C1-347–C1-348
Perekalina TM, Vinnik MA, Zvereva RI, Shchurova AD (1971) Magnetic properties of hexagonal ferrites with weak exchange coupling between sublattices. Sov Phys JETP 32:813–814
Glinchuk MD, Eliseev EA, Morozovska AN, Blinc R (2008) Giant magnetic effect induced by intrinsic surface stress in ferroic nanorods. Phys Rev B 77:024106
Acknowledgements
We thank A. N. Morozovska and E. A. Eliseev for critical remarks and A. E. Likhtin for technical assistance.
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Funding was provided by National Academy of Sciences of Ukraine (Projects III-8-16 and 44/18-H).
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Appendix
Appendix
Magnetization analysis
The solid solutions are materials with perovskite structure ABO3. We may rewrite the chemical formula as (PFT)x(PMN–PT)1−x = PbFex/2Tax/2Mg0.7(1−x)/3Nb1.4(1−x)/3Ti0.3(1−x)O3. Magnetic ions Fe and nonmagnetic M = Ta, Mg, Nb, Ti occupy the sites of cubic sublattice B with the percentage given by the corresponding subscript in the formula. The Fe ions may be distributed randomly or form some kind of short- or long-range chemical order. Evidence for partial chemical ordering in the B sublattice of complex perovskites comes from experiments [54,55,56,57] and theory [20,21,22, 58, 59]. Our NMR studies (see above) confirm the nonuniform distribution of Fe in the B sublattice.
Magnetic measurements for (PFT)x(PMN–PT)1−x with x = 0.1, 0.2, 0.3 (Fig. 10) show that these samples are in the paramagnetic state in the studied temperature range. Thus, we omitted any additional investigations of these samples and focused our attention on samples with x = 0.4 and 0.5.
We assume that a part of Fe3+ ions xFe < x/2 contribute to the paramagnetic response χp(T), another part, xs= x/2 − xFe, participates in superparamagnetic response. The Curie constant
gives the number Np of Fe spins (per 1 g of the material) in the paramagnetic state; μB is Bohr magneton. Figure 8 shows that these numbers are very close for both samples Np ≈ 2.8 × 1020. Using the molar mass of the solid solution mM(x), we find xFe = mM(x)Np/NA ≈ 0.16 for both samples, NA is the Avogadro number.
After that, we fit M(H) curves by the sum of paramagnetic and superparamagnetic contributions (cf. Eq.~(3) from Ref. [45]) given by Eq. (2).
We assume that the distribution of superspin moments is sharply peaked at the value μs(T) (i.e., all superspins are equal). Noting that L(x) → 1, for x → ∞, and \( \left. {\frac{\partial L(x)}{\partial x}} \right|_{x = 0} = \frac{1}{3} \), we may obtain the superspin moment value, and the number of superspins
from the slope of the superparamagnetic contribution to the isotherm curve at the origin \( \left. {\frac{{\partial M_{s} \left( {H,T} \right)}}{\partial H}} \right|_{H = 0} \) = (7.5 ± 0.6) × 10−4 emu (g Oe)−1 and saturated value of the superparamagnetic magnetization at large field Ms(∞,T) = 0.240 ± 0.003 emu g−1, for T = 293 K. For the other isotherms, we find (assuming that Ns does not change with T)
where Ms(∞,T) = 0.323 ± 0.003, 0.385 ± 0.003 emu g−1, for T = 193 K, 120 K.
Equations (6), (7) allow to find the number Ns and the value μs(T) for our samples. The M(H) curves for 04PFT sample are well fitted by Eq. (2) with the parameter values, Ns = 6.3 × 1014, μs(T)/μB = 6.6 × 104, 5.5 × 104, 4.1 × 104 for T = 120, 193, 293 K, respectively.
Assuming that the superspin moments display a mean-field like temperature dependence \( \mu_{\text{s}} (T) = \mu_{\text{s}} (0)\sqrt {1 - T/T_{\text{c}} } \), we obtain μs(0)/μB ≈ 7.9 × 104, Tc ≈ 400 K.
For x = 0.5, \( \left. {\frac{{\partial M_{s} \left( {H,293} \right)}}{\partial H}} \right|_{H = 0} \) = 1.5 × 10−4 emu (g Oe)−1, Ms(∞,T) = 0.089, 0.072, 0.058 emu g−1 for T = 120, 193, 293 K, respectively. It gives Ns= 1.8 · 1014, μs(T)/μB= 4.8 × 104, 4.3 × 104, 3.5 × 104 for T = 120, 193, 293 K, μs(0)/μB≈ 5.5 × 104, Tc ≈ 490 K.
Let us consider the possibility to explain the superparamagnetism of our samples by magnetic impurity phases. In Refs. [50, 51], the hysteresis loops in PFT and solid solutions PFT–PbTiO3 were supposed to be due to the presence of lead hexaferrite (magnetoplumbite) PbFe12O19. At room temperature, the saturation magnetization of the hexaferrite is ~ 50 emu g−1 [60, 61], or 0.88μB per Fe spin. Thus, ns12 = 4.7 × 104 of Fe spins in a particle of PbFe12O19 would have a magnetic moment μs(T)/μB = 4.1 × 104 at T = 293 K that would explain the superparamagnetism of 04PFT sample (see fourth row of Table 2). The size of the particle would be ~ 110 Å, because the volume of PbFe12O19 unit cell is 695 Å3 [62] and it contains 2 formula units, i.e., 24 Fe ions. Then the volume fraction of PbFe12O19 in our sample would be 0.7% and the mass fraction—0.48%; it can not be detected by XRD. But, as we have mentioned in the “Discussion” section, such a small fraction of the magnetic impurity phase can not produce appreciable ME response for two-phase composite material [53]. Also, against the presence of this impurity in our samples is the fact that the Curie temperature of bulk PbFe12O19 is 720 K [60, 63], which can be reduced in nanoparticles, but seems to be still much larger than Tc= 400–490 K found by us. If nonmagnetic ions substitute for Fe in the hexaferrite, the Curie temperature and the saturation magnetization are reduced dramatically [64,65,66,67]. In order to explain the superparamagnetism in our samples by such a diluted magnetoplumbite impurity, we would have to assume a larger fraction of the impurity phase, which is not observed by XRD.
In Ref. [52], the pyrochlore Pb3FeTaO7 impurity was supposed to be responsible for room-temperature hysteresis in PFT–PT solid solutions. Pb3FeTaO7 has 8 formula units in the cubic unit cell with a = 10.5 Å. The saturation magnetization at room temperature is ~ 2.7 emu g−1. We obtain ns,pyr = 8.8 · 104 of Fe spins in a particle. The particle size is 233 Å, the volume fraction is ~ 7%, and the mass fraction is 9%. But our samples have no more than 2.4% of the pyrochlore admixture.
Therefore, neither PbFe12O19 nor Pb3FeTaO7 can be responsible for the magnetism and magnetoelectricity of the considered materials.
Magnetoelectric coupling
Within a phenomenological Landau–Ginzburg–Devonshire approach, linear and biquadratic ME couplings contribution to the system free energy are described by the terms μijPiMj and ξijklPiPjMkMl, respectively (P is polarization and M is magnetization, and μij and ξijkl are corresponding tensors of linear and biquadratic ME effects, respectively) [10, 19, 68]. In ceramics, the elements of the tensors are averaged and we are dealing with scalar LGD equations. If we start the description from the symmetric paraelectric paramagnetic phase, we should retain only biquadratic ME coupling
where ξMP is the coupling parameter that is assumed to weakly depend on temperature. The terms FP and FM depend only on polarization and magnetization, respectively. For the second-order phase transitions they have the usual form in SI units system
where only αP,M have strong temperature dependence α ~ (T – TC). For small external fields, we may write the solutions of Eq. (8) in the form
where Ps, Ms are spontaneous polarization and magnetization that become nonzero in the ordered phases; χE,M are dielectric and magnetic susceptibilities. Then ME coupling has the form
that allows us to express various magnetoelectric coefficients via ξMP
Due to the superparamagnetic contribution, the value of β will increase with temperature lowering according to the temperature dependence of magnetic susceptibility as [χM(T)]2 ~ 1/T2.
Using the value of β(T) obtained from experiments, we can estimate the biquadratic ME coefficient ξMP from the equation
We got ξMP ≈ –2.9 × 10−5 J m3 A−2 C−2 for the solid solution with x = 0.4 by substituting the room temperature values of parameters: β ≈ 0.15 × 10−15 s A−1, the spontaneous electric polarization Ps≈3.0 μC cm−2, susceptibilities dielectric χFE ≈2000, and magnetic (mass) χM ≈0.63 emu (g kOe)−1. For x = 0.5, we have obtained ξMP≈ − 0.0014 J m3 A−2 C−2, using β ≈ 0.54 × 10−15 s A−1, Ps≈ 4.4 μC cm−2, χFE ≈2000, χM ≈0.142 emu (g kOe)−1. All parameters were determined from the data of our experiments reported in previous sections.
Let us note that Eq. (11) is appropriate for the description of the paramagnetic phase in small fields where magnetization is proportional to H. For the description of the superparamagnetic phase at higher fields, we should consider another expression for the free energy part FM
where \( Z = {{\sinh \left[ {\frac{{2\left( {S + 1} \right)\mu_{\text{s}} \left( T \right)H}}{{2Sk_{\text{B}} T}}} \right]} \mathord{\left/ {\vphantom {{\sinh \left[ {\frac{{2\left( {S + 1} \right)\mu_{\text{s}} \left( T \right)H}}{{2Sk_{\text{B}} T}}} \right]} {\sinh \left[ {\frac{{\mu_{\text{s}} \left( T \right)H}}{{2Sk_{\text{B}} T}}} \right]}}} \right. \kern-0pt} {\sinh \left[ {\frac{{\mu_{\text{s}} \left( T \right)H}}{{2Sk_{\text{B}} T}}} \right]}} \) is the partition function for an isolated spin S in the magnetic field H. For S ≫ 1 this gives \( M_{\text{s}} \left( {H,T} \right) = - {{\partial F_{\text{M}} } \mathord{\left/ {\vphantom {{\partial F_{\text{M}} } {\partial H}}} \right. \kern-0pt} {\partial H}} \), Eq. (2). We will neglect the contribution from paramagnetic phase. Then instead of Eq. (14) we have
and
In the experiment, the ME effect is manifested as a polarization Pac induced by a small ac magnetic field hac under application of dc field Hdc. With using collinear dc and ac magnetic fields H = Hdc + hac sin ωt, we obtain a generalization of Eq. (4)
Hence, the generalization of Eq. (5) shows that the amplitude of magnetoelectric current IME is proportional to dM2/dH (see inset in Fig. 9a).
The above consideration can only provide a qualitative agreement with the experiment. A more realistic theory should take into account at least a distribution of moment values.
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Glinchuk, M.D., Kuzian, R.O., Zagorodniy, Y.O. et al. Room-temperature ferroelectricity, superparamagnetism and large magnetoelectricity of solid solution PbFe1/2Ta1/2O3 with (PbMg1/3Nb2/3O3)0.7(PbTiO3)0.3. J Mater Sci 55, 1399–1413 (2020). https://doi.org/10.1007/s10853-019-04158-4
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DOI: https://doi.org/10.1007/s10853-019-04158-4