SrTiO 3 —Glimpses of an Inexhaustible Source of Novel Solid State Phenomena

: The purpose of this selective review is primarily to demonstrate the large versatility of the insulating quantum paraelectric perovskite SrTiO 3 explained in “Introduction” part, and “Routes of SrTiO 3 toward ferroelectricity and other collective states” part. Apart from ferroelectricity under various boundary conditions, it exhibits regular electronic and superconductivity via doping or external fields and is capable of displaying diverse coupled states. “Magnetoelectric multiglass (Sr,Mn)TiO 3 ” part, deals with mesoscopic physics of the solid solution SrTiO 3 :Mn 2 + . It is at the origin of both polar and spin cluster glass forming and is altogether a novel multiferroic system. Independent transitions at different glass temperatures, power law dynamic criticality, divergent third-order susceptibilities, and higher order magneto-electric interactions are convincing fingerprints.


Introduction
In this review, we focus onto two research lines of strontium titanate, SrTiO 3 (STO): (1) the low-temperature phases around the quantum critical point of pure STO, and (2) the disordered electric and magnetic dipolar glassy phases in the solid solution STO: Mn. It is not intended to describe the full extent of all phenomena observed and to detail all of their properties from abundantly issued publications. We merely try to give an impression of some actual fields, which are partially related to our earlier cooperation with K. A. Müller and J. G. Bednorz. STO is probably the most versatile perovskite-type oxide and one of the richest materials in terms of functionalities. In 1979, Müller and Burkard [1] reported that the planar permittivity of STO strongly increased upon cooling from ≈ 300 at room temperature and saturated with ε 110 ≈ 2.5·10 4 as T → 0 (comparable to ε 100 vs. T, cf. Figure 1, curve 1 [2]). They conjectured a "quantum paraelectric" ground state in close proximity to a ferroelectric (FE) one, where the centrosymmetric tetragonal lattice structure of STO becomes stabilized by quantum fluctuations of the nearly softening in-plane F 1u lattice mode.
Quantum corrections to the temperature were proposed to describe the critical behavior of STO from the beginning [1]. In order to account for the obvious deviations from the mean-field Curie-Weiss behavior, some of us proposed a generalized modified "quantum Curie-Weiss law" [3].  [2].
Quantum corrections to the temperature were proposed to describe the critical behavior of STO from the beginning [1]. In order to account for the obvious deviations from the mean-field Curie-Weiss behavior, some of us proposed a generalized modified "quantum Curie-Weiss law" [3].
where C stands for the Curie constant, γ for the critical exponent, and = coth( ⁄ ) for the quantum critical temperature with classic critical temperature and saturation temperature being related to the ground state energy of the quantum oscillator, = . Crucial novel ingredients are the free parameter γ and the quantum temperature scale, = coth( ⁄ ), which replaces T. The best fit to the STO data [3] within 2 ≤ T ≤ 110 K yields C = (3 ± 2) 10 6 , = (17 ± 1) K, ≈ 0, and the highly non-classic exponent γ = 1.7 ± 0.2. Interestingly, a very similar value, γ ≈ 2, was recently obtained on pure STO from a conventional power-law fit for 4 ≤ T ≤ 50 K [4], where saturation effects deviated below ≈ 4 K. While our approach matches with this extreme quantum regime without any extra conditions, the  model of [4] requires corrections due to long-range dipolar interactions and coupling of the electric polarization field to acoustic phonons.

Routes of SrTiO3 Toward Ferroelectricity and Other Collective States
Overcoming quantum paraelectricity and reaching stable long-range ordered states by proper treatments has remained a major challenge for ongoing research on STO.
(i) In 1976, Uwe and Sakudo [5] succeeded in stabilizing uniaxial ferroelectricity in STO at liquid He temperature by intraplanar symmetry breaking with uniaxial stress perpendicularly to the c axis, . This was the first experience to overcome quantum paraelectricity of STO by an external perturbation. (ii) About 20 years later, in 1999, Itoh et al. [6] discovered a very efficient internal perturbation via isotopic exchange of 16 O by 18 O in order to establish the FE state at T0 ≈ 25-50 K. (iii) Again, 20 years later, in 2019, Nova et al. [7] realized transient FE in STO being metastable up to T > 290 K under optical strain due to intense femtosecond laser pulses, while Li et al. [8] recorded similar events after photoexcitation of quantum paraelectric STO with THz laser pulses in resonance with the FE soft mode at T < 36 K. (iv) Metallic behavior of n-type STO has been achieved by substituting transition-metal dopants, e.g., La 3+ for Sr 2+ [9], Nb 5+ for Ti 4+ , or by reducing pure STO into SrTiO3-δ, 0 < δ < 1, where each oxygen where C stands for the Curie constant, γ for the critical exponent, and T Q 0 = T S cot h(T S /T 0 ) for the quantum critical temperature with classic critical temperature T 0 and saturation temperature T S being related to the ground state energy of the quantum oscillator, E 0 = k B T S . Crucial novel ingredients are the free parameter γ and the quantum temperature scale, T Q = T S cot h(T S /T), which replaces T. The best fit to the STO data [3] within 2 ≤ T ≤ 110 K yields C = (3 ± 2) 10 6 , T S = (17 ± 1) K, T Q 0 ≈ 0, and the highly non-classic exponent γ = 1.7 ± 0.2. Interestingly, a very similar value, γ ≈ 2, was recently obtained on pure STO from a conventional power-law fit for 4 ≤ T ≤ 50 K [4], where saturation effects deviated below ≈ 4 K. While our approach matches with this extreme quantum regime without any extra conditions, the Φ 4 model of [4] requires corrections due to long-range dipolar interactions and coupling of the electric polarization field to acoustic phonons.

Routes of SrTiO 3 toward Ferroelectricity and Other Collective States
Overcoming quantum paraelectricity and reaching stable long-range ordered states by proper treatments has remained a major challenge for ongoing research on STO.
(i) In 1976, Uwe and Sakudo [5] [8] recorded similar events after photoexcitation of quantum paraelectric STO with THz laser pulses in resonance with the FE soft mode at T < 36 K. (iv) Metallic behavior of n-type STO has been achieved by substituting transition-metal dopants, e.g., La 3+ for Sr 2+ [9], Nb 5+ for Ti 4+ , or by reducing pure STO into SrTiO 3-δ , 0 < δ < 1, where each oxygen vacancy generates two "doped" electrons [10]. The insulator-to-metal transformation occurs at a relatively low critical electron density n ≈ 10 18 cm −3 [11], i.e., two orders of magnitude less than in the analogous case of barium titanate [12]. Here the word "metal" is not used in its common material meaning but merely stands for featuring metallic electronic conduction.

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A combined method of substitution and reduction was utilized in the case of Cr-doped STO [11]. A significant spatial correlation between oxygen vacancies and Cr 3+ ions in bulk was established in thermally reduced Cr-doped STO. In the presence of electron donors, the Cr atoms change their valence from 4+ to 3+. Consequently, this reduction drives a symmetry change of the crystal field experienced by the Cr ions from cubic to axial [11], which may be controlled by means of thermal annealing and/or doping with electron donors. This capability of controlling oxygen vacancies or transition-metal dopants has been essential for the development of semiconducting electronic devices [13]. (v) Theoretical predictions of superconductivity in degenerate semiconductors motivated research on reduced n-type STO, which revealed the critical temperature T c ≈ 0.28 K as early as 1964 [14]. However, 32 years later, perovskite-like cuprates were to open the door to modern high-T c superconductivity with T c ≈ 30 K [15] and to the physics Nobel Prize [16]. On the other hand, gated n-type STO has reached at most only T c ≈ 0.6 K [17].
Meanwhile numerous other processes have made STO a nearly inexhaustible source of activating novel solid state phenomena that suggest future applications. This has remained an attractive research goal even more than 60 years after the pioneering experiments. Extending the initial idea of breaking the local symmetry by stress [5], Bednorz and Müller [2] introduced an A-site doping route by random replacement of Sr 2+ ions with smaller Ca 2+ ions in single crystals of Sr 1-x Ca x TiO 3 (SCT). The local decrease of volume creates random strain ("negative stress field"), which has an enormous effect on the dielectric response for doping levels 0.002 ≤ x ≤ 0.12, as shown in Figure 1 (curves 2-11). Sharp peaks occur at finite temperatures, 10 < T m < 40 K, which clearly hint at polar phase transitions (PTs). Their easy axes are actually lying along [110] and [110] within the basal xy-plane and yield, e.g., ε 110 max = 1.1·10 5 for x = 0.0107 [2]. Discussion within a random-field concept of PTs reveals xy-type quantum ferroelectricity above x c = 0.0018 along the a axes of the paraelectric parent phase and a PT into a random phase above x r ≈ 0.016 ( Figure 1). Quantum corrections to the temperature (see Equation (1)) are essential to describe the critical behavior.
In order to understand more details, some of us measured the optical linear birefringence (LB), ∆n ac = n c − n a , where n c and n a are the principal refractive indices at light wavelength λ = 589.3 nm, being linearly polarized along the c and a axes of the SCT crystal, respectively, as functions of temperature, T [18]. It is well-known that the LB is sensitive to both the axial rotation of the TiO 6 octahedra, <∆Φ 2 >, below the antiferrodistortive phase transition temperature T a = 105 K (for x = 0), and to the FE short-range order parameter, <P 2 x >, where x <110> c ( Figure 1). Indeed, non-zero LB arises in pure STO at the transition temperature T a = 105 K and at 115, 140, and 255 K (arrows) for x = 0.002, 0.0107, and 0.058, respectively, as shown in Figure 2. Additional FE anomalies, δ(∆n ac ), are superposed at low T. Being non-morphic, they start smoothly with fluctuation tails and bend over into steeply rising long-range order parts below inflection points T 1 ≈ 15, 28, and 50 K, respectively (arrows). These temperatures systematically exceed the ε vs. T peak temperatures, T m = 14, 26, and 35 K, respectively (Figure 1), where discontinuities of d(∆n ac )/dT would be expected in case of PTs into long-range order. Absence of anomalies of this type and increasing differences, T 1 -T m , at increasing x hint at continuously growing smearing of the PTs. Simultaneously, as T → 0, the polarization was calculated by use of the ordinary refractive index n o = 2.41 and the electro-optic coefficient difference g 11 -g 31 = 0.14 m 4 /C 2 as < P 2 x > 1/2 = {2δ(∆n ac )/[n o 3 (g 11 -g 31 )]} = 9.8, 29.4, and 42.6 mC/m 2 for x = 0.002, 0.0107, and 0.058, respectively [18]. Since < P 2 x > 1/2 varies less than proportionally with x, comparatively incomplete FE order is observed. Further, the low-T polarization saturates, albeit slowly, at increasing electric field, E. This strongly hints at random-field induced nanodomains, whose average size increases with an applied ordering field. The increase of the average order parameter gives credit for disappearing domain walls as known from the domain-state FE K 0.974 Li 0.026 TaO 3 [19]. Further insight into FE SCT is gained from its relaxational behavior. Figure 3 shows the temperature dependence of the real and imaginary parts of the dielectric permittivity of SCT (x = 0.002), , and ″ vs. T, at frequencies 10 3 ≤ f ≤ 10 4 Hz [20]. In view of the rounded peaks of (T), a polydomain state of this FE is conjectured. This has first been interpreted within the concept of "dynamical heterogeneity" [21], which assumes a manifold of mesoscopic "dynamically correlated domains", relaxing exponentially with uniform single relaxation times. Their superposition defines the observed polydispersivity of the sample. It represents aggregates of polar clusters surrounding the quenched off-center Ca 2+ dopant dipoles.
It is noticed that vs. T peaks at a "glass temperature", Tg ≈ 3.8 K (Figure 3, arrow), in the quasistatic limit, f = 1 mHz, although at first glance, no glassy criticality as in spin glass is expected. However, in view of recently ascertained magnetic superspin glasses (SSG) of dipolarly coupled magnetic nanoparticles at low concentration [22], a related electric superdipolar glass (SDG) has become envisaged. It should behave like a relaxor ferroelectric [23] in terms of a superglassy critical power law behavior of the ε( ) vs. T peak position Tm.
Evaluation over the whole range of frequencies, 10 −3 ≤ f ≤ 10 4 Hz, yields the expected dynamic critical exponent zν ≈ 10 at f > 1Hz, while systematic deviations occur at lower f due to the well-known additional tunneling dynamics. Tests on the expected non-ergodicity of the SDG phase at T < Tg upon zero-field-and field-cooled temperature cycles, respectively (cf. Section 3) are in preparation.  Further insight into FE SCT is gained from its relaxational behavior. Figure 3 shows the temperature dependence of the real and imaginary parts of the dielectric permittivity of SCT (x = 0.002), ε , and ε vs. T, at frequencies 10 3 ≤ f ≤ 10 4 Hz [20]. In view of the rounded peaks of ε (T), a polydomain state of this FE is conjectured. This has first been interpreted within the concept of "dynamical heterogeneity" [21], which assumes a manifold of mesoscopic "dynamically correlated domains", relaxing exponentially with uniform single relaxation times. Their superposition defines the observed polydispersivity of the sample. It represents aggregates of polar clusters surrounding the quenched off-center Ca 2+ dopant dipoles. Further insight into FE SCT is gained from its relaxational behavior. Figure 3 shows the temperature dependence of the real and imaginary parts of the dielectric permittivity of SCT (x = 0.002), , and ″ vs. T, at frequencies 10 3 ≤ f ≤ 10 4 Hz [20]. In view of the rounded peaks of (T), a polydomain state of this FE is conjectured. This has first been interpreted within the concept of "dynamical heterogeneity" [21], which assumes a manifold of mesoscopic "dynamically correlated domains", relaxing exponentially with uniform single relaxation times. Their superposition defines the observed polydispersivity of the sample. It represents aggregates of polar clusters surrounding the quenched off-center Ca 2+ dopant dipoles.
It is noticed that vs. T peaks at a "glass temperature", Tg ≈ 3.8 K (Figure 3, arrow), in the quasistatic limit, f = 1 mHz, although at first glance, no glassy criticality as in spin glass is expected. However, in view of recently ascertained magnetic superspin glasses (SSG) of dipolarly coupled magnetic nanoparticles at low concentration [22], a related electric superdipolar glass (SDG) has become envisaged. It should behave like a relaxor ferroelectric [23] in terms of a superglassy critical power law behavior of the ε( ) vs. T peak position Tm.
Evaluation over the whole range of frequencies, 10 −3 ≤ f ≤ 10 4 Hz, yields the expected dynamic critical exponent zν ≈ 10 at f > 1Hz, while systematic deviations occur at lower f due to the well-known additional tunneling dynamics. Tests on the expected non-ergodicity of the SDG phase at T < Tg upon zero-field-and field-cooled temperature cycles, respectively (cf. Section 3) are in preparation.  It is noticed that ε vs. T peaks at a "glass temperature", T g ≈ 3.8 K (Figure 3, arrow), in the quasi-static limit, f = 1 mHz, although at first glance, no glassy criticality as in spin glass is expected. However, in view of recently ascertained magnetic superspin glasses (SSG) of dipolarly coupled magnetic nanoparticles at low concentration [22], a related electric superdipolar glass (SDG) has become envisaged. It should behave like a relaxor ferroelectric [23] in terms of a superglassy critical power law behavior of the ε ( f ) vs. T peak position T m .
Evaluation over the whole range of frequencies, 10 −3 ≤ f ≤ 10 4 Hz, yields the expected dynamic critical exponent zν ≈ 10 at f > 1Hz, while systematic deviations occur at lower f due to the well-known additional tunneling dynamics. Tests on the expected non-ergodicity of the SDG phase at T < T g upon zero-field-and field-cooled temperature cycles, respectively (cf. Section 3) are in preparation.
At higher concentration of Ca 2+ , the polar nanoregions (PNRs) percolate into an FE ground state, as proven by first-order Raman scattering at the softening F 1u phonon mode in SCT (x = 0.007) at T < T 0 = 18 K [24]. SCT thus succeeds in demonstrating stable ferroelectricity. However, systematic research at increasing Ca content showed that T 0 is limited to ≈35 K, where the dielectric anomaly becomes increasingly smeared [25]. Better success was achieved by the classic method of stress-induced ferroelectricity in pure STO [5]. To this end Haeni et al. [26] utilized 50 nm thick films of STO, which were epitaxially grown with approximately +1.5% biaxial tensile strain on a (110) DyScO 3 substrate, while −0.9% uniform compression due to a (LaAlO 3 ) 0.29 (SrAl 0.5 Ta 0.5 O 3 ) 0.71 (LSAT) substrate was barely active in this respect ( Figure 4). The high permittivity in the films on DyScO 3 , ε up to 7000 at 10 GHz and room temperature, as well as its sharp dependence on an electric field is promising for device applications [4,26]. The observation of stress-induced ferroelectricity in STO films has confirmed theoretical predictions of Pertsev et al. [27]. While substrate induced tensile strain in epitaxial STO films via lattice parameter mismatch favors in-plane FE, compressive strain provides out-of-plane directed ferroelectricity [27]. This was observed by Fuchs et al. [28] at an STO film epitaxially grown on an STO substrate coated by compressive YBa 2 Cu 3 O 7 .
ndens. Matter 2020, 5, 58 5 of At higher concentration of Ca 2+ , the polar nanoregions (PNRs) percolate into an FE ground sta proven by first-order Raman scattering at the softening phonon mode in SCT (x = 0.007) at T0 = 18 K [24]. SCT thus succeeds in demonstrating stable ferroelectricity. However, systema search at increasing Ca content showed that T0 is limited to ≈35 K, where the dielectric anoma ecomes increasingly smeared [25]. Better success was achieved by the classic method of stres duced ferroelectricity in pure STO [5]. To this end Haeni et al. [26] utilized 50 nm thick films O, which were epitaxially grown with approximately +1.5% biaxial tensile strain on a (110) DySc bstrate, while −0.9% uniform compression due to a (LaAlO3)0.29(SrAl0.5Ta0.5O3)0.71 (LSAT) substra as barely active in this respect (Figure 4). The high permittivity in the films on DyScO3, up 00 at 10 GHz and room temperature, as well as its sharp dependence on an electric field romising for device applications [4,26]. The observation of stress-induced ferroelectricity in ST lms has confirmed theoretical predictions of Pertsev et al. [27]. While substrate induced tensile stra epitaxial STO films via lattice parameter mismatch favors in-plane FE, compressive strain provid t-of-plane directed ferroelectricity [27]. This was observed by Fuchs et al. [28] at an STO fil itaxially grown on an STO substrate coated by compressive YBa2Cu3O7. Another realization of room temperature ferroelectricity in STO confirms theoretical predictio proximity effects at interfaces of metals to oxides containing PNRs such as, for example, STO [2 ee et al. [30] reported emergence of room temperature ferroelectricity at reduced dimensions, th futing a long-standing contradicting notion. Piezoelectric force microscopy (PFM) was able idence room-temperature ferroelectricity in strain-free epitaxial films with 24 unit-cell-thickness herwise non-ferroelectric STO ( Figure 5). Following arguments from defect engineering in SCT, t thors claimed that electrically induced alignments of PNRs at Sr deficiency related defects a sponsible for the appearance of a stable net of ferroelectric polarization in these films. This insig ight be useful for the development of low-D materials of emerging nanoelectronic devices. Another realization of room temperature ferroelectricity in STO confirms theoretical predictions of proximity effects at interfaces of metals to oxides containing PNRs such as, for example, STO [29]. Lee et al. [30] reported emergence of room temperature ferroelectricity at reduced dimensions, thus refuting a long-standing contradicting notion. Piezoelectric force microscopy (PFM) was able to evidence room-temperature ferroelectricity in strain-free epitaxial films with 24 unit-cell-thickness of otherwise non-ferroelectric STO ( Figure 5). Following arguments from defect engineering in SCT, the authors claimed that electrically induced alignments of PNRs at Sr deficiency related defects are responsible for the appearance of a stable net of ferroelectric polarization in these films. This insight might be useful for the development of low-D materials of emerging nanoelectronic devices.
To systematically control ferroelectricity in thin films of STO at room temperature, Kang et al. [31] selectively engineered elemental vacancies by pulsed laser epitaxy (PLE). Sr 2+ vacancies play an essential role in inducing the cubic-to-tetragonal transition, since they break the inversion symmetry, which is necessary for switchable electric polarization. The tetragonality turns out to increase with increasing vacancy density, thus strengthening the ferroelectricity, as shown in Figure 6a. This research has optimized tetragonality-induced ferroelectricity in STO with reliable growth control of the behavior. PFM yields stable hysteresis loops at room temperature, as shown in Figure 6b, where low and high laser fluences during PLE clearly demonstrate their key role in creating FE polarization. Similar propositions were made by the Barthélémy-Bibes group, which invoked both an electric field-switchable two-dimensional electron gas emerging in ferroelectric SCT films [32] and the non-volatile electric control of spin-charge conversion in an STO Rashba system [33].
Another realization of room temperature ferroelectricity in STO confirms theoretical predictions of proximity effects at interfaces of metals to oxides containing PNRs such as, for example, STO [29]. Lee et al. [30] reported emergence of room temperature ferroelectricity at reduced dimensions, thus refuting a long-standing contradicting notion. Piezoelectric force microscopy (PFM) was able to evidence room-temperature ferroelectricity in strain-free epitaxial films with 24 unit-cell-thickness of otherwise non-ferroelectric STO ( Figure 5). Following arguments from defect engineering in SCT, the authors claimed that electrically induced alignments of PNRs at Sr deficiency related defects are responsible for the appearance of a stable net of ferroelectric polarization in these films. This insight might be useful for the development of low-D materials of emerging nanoelectronic devices. Figure 5. Polarization hysteresis of 24 and 120 unit-cell-thick STO films at room temperature, measured by using the double-wave PUND technique with a triangular ac electric field of 10 kHz (see schematic inset). The hysteresis component is obtained by subtracting the non-hysteretic (up (U) and down (D)) from the total (positive (P) and negative (N)) polarization runs [30]. To systematically control ferroelectricity in thin films of STO at room temperature, Kang et al. [31] selectively engineered elemental vacancies by pulsed laser epitaxy (PLE). Sr 2+ vacancies play an essential role in inducing the cubic-to-tetragonal transition, since they break the inversion symmetry, which is necessary for switchable electric polarization. The tetragonality turns out to increase with increasing vacancy density, thus strengthening the ferroelectricity, as shown in Figure 6a. This research has optimized tetragonality-induced ferroelectricity in STO with reliable growth control of the behavior. PFM yields stable hysteresis loops at room temperature, as shown in Figure 6b, where low and high laser fluences during PLE clearly demonstrate their key role in creating FE polarization. Similar propositions were made by the Barthélémy-Bibes group, which invoked both an electric fieldswitchable two-dimensional electron gas emerging in ferroelectric SCT films [32] and the non-volatile electric control of spin-charge conversion in an STO Rashba system [33]. Only recently has another insight into the ferroelectric state of compressively strained STO become available from high-angle annular dark-field imaging in scanning transmission electron microscopy. Salmani-Rezaie et al. [34] observed local polar regions in the room-temperature paraelectric phase of (001)-strained STO films, which were grown on (001) faces of LSAT and underwent an FE transition at low T. This unexpected feature was explained by a locally dipolarordered, but globally random phase of displaced Ti 4+ columns, which underwent a disorder-order transition on cooling.
This Section started with different methods to establish long-range order, such as ferroelectricity (FE), metallicity (MT), or superconductivity (SC) in suitably modified STO [2,9,14]. Lately, more Only recently has another insight into the ferroelectric state of compressively strained STO become available from high-angle annular dark-field imaging in scanning transmission electron microscopy. Salmani-Rezaie et al. [34] observed local polar regions in the room-temperature paraelectric phase of (001)-strained STO films, which were grown on (001) faces of LSAT and underwent an FE transition at low T. This unexpected feature was explained by a locally dipolar-ordered, but globally random phase of displaced Ti 4+ columns, which underwent a disorder-order transition on cooling.
This Section started with different methods to establish long-range order, such as ferroelectricity (FE), metallicity (MT), or superconductivity (SC) in suitably modified STO [2,9,14]. Lately, more demanding procedures have become successful to stabilize the co-existence of apparently contradictory properties, e.g., FE-SC and FE-MT, which appear self-excluding at first glance. In this context, obscure terms such as, for example, "polar metal" and "metallic ferroelectric" or "ferroelectric metal" have been used interchangeably by the research community. Only recently have subtle distinctions of these variants with respect to their electric field switchability been clarified [12], although this topic still remains under debate.
Rischau et al. [35] showed that SC can coexist with an FE-like instability in oxygen-reduced ("n-doped") Sr 1-x Ca x TiO 3-δ (0.002 < x < 0.009, 0 < δ < 0.001), where both long-range orders are intimately linked. The FE transition of insulating SCT was found to survive in this reduced modification. Owing to its metallic conductivity, the latter does not show a bulk reversible electric polarization and hence cannot be a true ferroelectric. However, it shows anomalies in various physical properties at the Curie temperature of the insulator, e.g., Raman scattering evidences that the hardening of the FE soft mode in the dilute metal is identical with what is seen in the insulator. The anomaly in resistivity was found to terminate at a threshold carrier density (n*), near to which the SC transition temperature is enhanced [35]. This evidences the link between SC pairing and FE dipolar ordering, a subject of current attention [36].
Moreover, it is widely accepted that the low-T phase of STO lies in the vicinity of a quantum critical point, where different phases (i.e., paraelectric, antiferrodistortive, FE, MT, and SC) with similar energies compete, while weak residual interactions may stabilize one or several of these states [37][38][39]. The coexistence of MT and FE states in STO has been addressed under the keyword charge transport in a polar metal by Wang et al. [40], who studied the low-T electrical resistivity in several Sr 1-x Ca x TiO 3-δ single-crystals at δ > 0 within 0.002 < x < 0.01 (Figure 7). Since both MT and FE are dilute, the distance between mobile MT electrons and fixed FE dipoles can be separately tuned but kept much longer than the interatomic distance. This opens the chance of activating a Ruderman-Kittel-Kasuya-Yosida-like interaction [41] of carriers with local electric moments, which was originally proposed by Glinchuk and Kondakova [42]. They introduced this indirect interaction of FE off-center ions with conduction electrons in order to explain high FE transition temperatures in certain narrow-gap semiconductors with high conductivity, such as Pb 1-x Ge x Te. In agreement with this theory, it is expected that the threshold concentration of carriers, n*, is proportional to x, which indicates that it occurs at a fixed ratio between inter-carrier and inter-dipole distances.
Condens. Matter 2020, 5, 58 7 of 12 cannot be a true ferroelectric. However, it shows anomalies in various physical properties at the Curie temperature of the insulator, e.g., Raman scattering evidences that the hardening of the FE soft mode in the dilute metal is identical with what is seen in the insulator. The anomaly in resistivity was found to terminate at a threshold carrier density (n*), near to which the SC transition temperature is enhanced [35]. This evidences the link between SC pairing and FE dipolar ordering, a subject of current attention [36]. Moreover, it is widely accepted that the low-T phase of STO lies in the vicinity of a quantum critical point, where different phases (i.e., paraelectric, antiferrodistortive, FE, MT, and SC) with similar energies compete, while weak residual interactions may stabilize one or several of these states [37][38][39]. The coexistence of MT and FE states in STO has been addressed under the keyword charge transport in a polar metal by Wang et al. [40], who studied the low-T electrical resistivity in several Sr1-xCaxTiO3-δ single-crystals at δ > 0 within 0.002 < x < 0.01 (Figure 7). Since both MT and FE are dilute, the distance between mobile MT electrons and fixed FE dipoles can be separately tuned but kept much longer than the interatomic distance. This opens the chance of activating a Ruderman-Kittel-Kasuya-Yosida-like interaction [41] of carriers with local electric moments, which was originally proposed by Glinchuk and Kondakova [42]. They introduced this indirect interaction of FE off-center ions with conduction electrons in order to explain high FE transition temperatures in certain narrowgap semiconductors with high conductivity, such as Pb1-xGexTe. In agreement with this theory, it is expected that the threshold concentration of carriers, n*, is proportional to x, which indicates that it occurs at a fixed ratio between inter-carrier and inter-dipole distances.   [2]) and in metallic Sr 1-x Ca x TiO 3-δ (δ > 0) as functions of charge carrier density n and x = 0.0022, 0.0045 and 0.009 (green, blue, and red balls, respectively [40]). Being arbitrarily close to the quantum critical point of non-centrosymmetric SC, experiments have thus come into reach to probe mixed-parity pairing mechanisms with topological aspects to their SC states, such as extremely large and highly anisotropic upper critical fields and topologically protected spin currents. A decisive step toward this aim was done by Schumann et al. [43] using La 3+ or Sm 3+ n-doped STO films on (001)-strained LSAT substrates. Being in their polar phase, they reveal enhanced superconducting T c , while some of them show signatures of an unusual SC state, where the in-plane critical field is higher than both the paramagnetic and orbital pair breaking limits. Moreover, nonreciprocal transport is observed, which reflects the ratio of odd versus even pairing interactions. A similar highlight was observed in a gate-induced 2D SC of interfacial STO [44]. Due to its Rashba-type spin orbit interaction, it reveals nonreciprocal transport, where the inequivalent rightward and leftward currents reflect simultaneous spatial inversion and time-reversal symmetry breaking-an exciting prospect of forthcoming research on STO.

The Magnetoelectric Multiglass (Sr,Mn)TiO 3
The nature of glassy states in disordered materials has long been controversially discussed. In the magnetic community, generic spin glasses have long been accepted to undergo phase transitions at a static glass temperature T g , where they exhibit criticality and originate well-defined order parameters [45]. In addition, disordered polar systems are expected to transit into generic "dipolar" or "orientational glass" states [46], which fulfil similar criteria as spin glasses. Hence, it appears quite natural to introduce the term "multiglass" for a new kind of multiferroic material revealing both polar and spin glass properties, which were discovered by some of us in the ceramic solid solution Sr 0.98 Mn 0.02 TiO 3 [47]. By various experimental methods [48][49][50] it has been ascertained that the Mn 2+ ions are randomly substituting Sr 2+ ions on A-sites in quantum paraelectric STO (Figure 8a), where they become off-centered due to their small ionic size and undergo covalent bonding with one of the twelve nearest neighboring O 2− ions. These elementary dipoles readily form polar nanoclusters with frustrated dipolar interactions, as illustrated in Figure 8b. It depicts the local cluster formation of Mn 2+ ions with antiparallel electric dipole moments and antiferromagnetically correlated spins.
Condens. Matter 2020, 5, 58 8 of 12 type spin orbit interaction, it reveals nonreciprocal transport, where the inequivalent rightward and leftward currents reflect simultaneous spatial inversion and time-reversal symmetry breaking-an exciting prospect of forthcoming research on STO.

The Magnetoelectric Multiglass (Sr,Mn)TiO3
The nature of glassy states in disordered materials has long been controversially discussed. In the magnetic community, generic spin glasses have long been accepted to undergo phase transitions at a static glass temperature Tg, where they exhibit criticality and originate well-defined order parameters [45]. In addition, disordered polar systems are expected to transit into generic "dipolar" or "orientational glass" states [46], which fulfil similar criteria as spin glasses. Hence, it appears quite natural to introduce the term "multiglass" for a new kind of multiferroic material revealing both polar and spin glass properties, which were discovered by some of us in the ceramic solid solution Sr0.98Mn0.02TiO3 [47]. By various experimental methods [48][49][50] it has been ascertained that the Mn 2+ ions are randomly substituting Sr 2+ ions on A-sites in quantum paraelectric STO (Figure 8a), where they become off-centered due to their small ionic size and undergo covalent bonding with one of the twelve nearest neighboring O 2− ions. These elementary dipoles readily form polar nanoclusters with frustrated dipolar interactions, as illustrated in Figure 8b. It depicts the local cluster formation of Mn 2+ ions with antiparallel electric dipole moments and antiferromagnetically correlated spins.  [46]. (b) Schematic structure of SrTiO3:Mn 2+ highlighting a percolating multiglass path of randomly distributed Mn 2+ ions (red-blue broken line) carrying dipole moments σj (blue lines) and spins Sj (red arrows) with electric dipolar and antiferromagnetic correlations, respectively, within polar STO clusters (red "clouds") [51].
The dipolar glass formation can easily be judged from the asymptotic shift of the dynamic dielectric susceptibility peak, ( ), at frequencies within the range 10 −1 ≤ f ≤ 10 6 Hz in Figure 9a. It The dipolar glass formation can easily be judged from the asymptotic shift of the dynamic dielectric susceptibility peak, T m ( f ), at frequencies within the range 10 −1 ≤ f ≤ 10 6 Hz in Figure 9a. It obeys glassy critical behavior according to Equation (2), where zν = 8.5 is the dynamic critical exponent and T e g ≈ 38 K the electric glass temperature [51]. On the other hand, frustrated and random Mn 2+ -O 2− -Mn 2+ superexchange is at the origin of spin glass formation below the magnetic glass temperature T m g ≈ 34 K. This temperature marks the confluence of three characteristic magnetization curves recorded in µ 0 H = 10 mT after zero-field cooling (ZFC) to T = 5 K upon field heating (m ZFC ), upon subsequent field cooling (m FC ), and thereafter the thermoremanence (m TRM ) upon zero-field heating (ZFH) as shown in Figure 9c. It should be noticed that both glassy states have unanimously been confirmed by clear-cut individual aging, rejuvenation, and memory effects in their respective dc susceptibilities [51]. "Holes" burnt into the electric and magnetic susceptibilities by waiting in zero external field for 10.5 h at 32.8 K and for 2.8 h at 33 K, respectively, and subsequent heating with weak electric or magnetic probing fields are shown in Figure 9b,d, respectively. They corroborate the glassy ground states of both polar and magnetic subsystems and their compatibility with spin glass theory [45]. Observation of the biquadratic ME interaction in the free energy [47], is compatible with the low symmetry of the compound and is thought to crucially reinforce the spin glass ordering, as schematically depicted in Figure 8b [51]. Similarly to the dielectric anomaly [52], the magnetic anomaly has been found to depend not only on the frequency, but crucially also on the Mn content, confirming its intrinsic origin [53]. Furthermore, apart from ceramics, both glassy states have also been detected in equivalent thin films [54].
Condens. Matter 2020, 5, 58 9 of 12 is compatible with the low symmetry of the compound and is thought to crucially reinforce the spin glass ordering, as schematically depicted in Figure 8b [51]. Similarly to the dielectric anomaly [52], the magnetic anomaly has been found to depend not only on the frequency, but crucially also on the Mn content, confirming its intrinsic origin [53]. Furthermore, apart from ceramics, both glassy states have also been detected in equivalent thin films [54]. Starting from a mean-field ansatz within the framework of a transverse Ising model [51], the complete theory of the ME multiglass is still under debate. In particular, the final steps for establishing the spin glass are missing. It is thought to emerge from multipolar interaction of spin clusters (Figure 8b) and probably comes close to the formation of a superspin glass as in systems of magnetic nanoparticles [22]. Since these probably consist of antiferromagnetic MnTiO3 and carry merely surface magnetization [55], special care has to be taken.
In search of other ME multiglasses, we successfully examined also Mn 2+ doped KTaO3, which in the undoped case is a quantum paraelectric like STO, but nevertheless has slightly different properties on doping [56]. Other research groups have made similar experiments, and all of them reported considerable complexity [57][58][59][60]. Moreover, various other ME multiglasses have also been observed in disordered solid solutions such as CuFe0.5V0.5O2 [61], La2NiMnO6 [62], Fe2TiO5 [63], and Starting from a mean-field ansatz within the framework of a transverse Ising model [51], the complete theory of the ME multiglass is still under debate. In particular, the final steps for establishing the spin glass are missing. It is thought to emerge from multipolar interaction of spin clusters (Figure 8b) and probably comes close to the formation of a superspin glass as in systems of magnetic nanoparticles [22]. Since these probably consist of antiferromagnetic MnTiO 3 and carry merely surface magnetization [55], special care has to be taken.