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Review Article | Open Access
J. C. Phillips, "Hard-Wired Dopant Networks and the Prediction of High Transition Temperatures in Ceramic Superconductors", Advances in Condensed Matter Physics, vol. 2010, Article ID 250891, 13 pages, 2010. https://doi.org/10.1155/2010/250891
Hard-Wired Dopant Networks and the Prediction of High Transition Temperatures in Ceramic Superconductors
I review the multiple successes of the discrete hard-wired dopant network model ZZIP, and comment on the equally numerous failures of continuum models, in describing and predicting the properties of ceramic superconductors. The prediction of transition temperatures can be regarded in several ways, either as an exacting test of theory, or as a tool for identifying theoretical rules for defining new homology models. Popular “first principle” methods for predicting transition temperatures in conventional crystalline superconductors have failed for cuprate HTSC, as have parameterized models based on planes (with or without apical oxygen). Following a path suggested by Bayesian probability, it was found that the glassy, self-organized dopant network percolative model is so successful that it defines a new homology class appropriate to ceramic superconductors. The reasons for this success in an exponentially complex (non-polynomial complete, NPC) problem are discussed, and a critical comparison is made with previous polynomial (PC) theories. The predictions are successful for the superfamily of all ceramics, including new non-cuprates based on FeAs in place of .
The prediction of transition temperatures is rightly considered to be one of the most difficult problems in theoretical physics. Here one should distinguish between a true (or bare) prediction (the value of is not known when the prediction is made), and a postdated calculation carried out according to certain rules after has been measured experimentally. If the rules (sometimes called “first principles”) have been established for similar materials, and they are faithfully applied to the new case, then the validity of the rules can be tested by the success of the prediction. If the number of example materials where the rules have been applied previously is large compared to the number of adjustable parameters, then the prediction can be said to be based on homology, namely, the supposed microscopic similarity of the phase transition of the new material to those previously studied.
Perhaps the best-known example of a “bare” prediction of a transition temperature was  for superfluidity of e. The predicted value of was 100 mK, whereas the measured value  of was 3.6 mK, so the predicted value was too large by a factor of 30. The most successful predated prediction of for superconductors based on homology was for the high-pressure phase of Si , where the experimental maximum is 8.2 K, and estimation of using the most popular rules gave = 5 K. A number of postdated predictions of superconductive have been made based on homology models and “first principles” rules. The rules depend mainly on the Fermi-surface average of the electron-phonon coupling constant and the phonon frequency squared . The most popular of these have been the prediction of in Mg based on homologies with simple metals such as Al, where the predicted and experimental values are both about 40 K . Equally impressive has been the prediction of in 5% B-doped CVD diamond, where the predicted and experimental values are = 22 K and = 11 K, respectively . The agreement here between theory and experiment is better than it appears to be, as some of the may have formed electrically inactive dimers. This example illustrates the strengths and limitations of homology arguments based on first principles, as the material properties of -doped CVD diamond are a far cry from those of single-crystal Al or Mg.
The success of crystalline models for electron-phonon interactions in Mg, and their failure in ceramic superconductors, is sometimes cited as “proof” that ceramic HTSC is not caused by electron-phonon interactions. This argument completely ignores the fact that doping is required to render ceramic materials metallic and superconductive, whereas substitutional doping of MgB2 drastically depresses . From these contrary chemical doping trends it is already obvious that something drastically different from crystalline superconductivity must be happening to cause ceramic HTSC. These drastic differences are likely to be caused by the strong disorder introduced by the dopants. Perhaps the most dramatic differences are apparent in the phase diagrams of in compared to , as shown in Figure 1. As both compounds are oxides, one might have expected to see similar phase diagrams, but clearly the standard parabolic of the cuprates is not seen in the triangular of . The latter is well understood: as decreases, the dopant free charge density decreases, and with it the screening of electron-phonon interactions, so increases right up to the metal-insulator transition. Our main task for the ceramic superconductors is now to explain the parabolic dependence of (which is not difficult in a glassy network model), and to predict at optimal doping (much harder).
Other examples of predictions are the proton order-disorder transition in high-pressure ice, where the predicted and experimental values are 98 K and 72 K, respectively (KOH doping) , and strained thin-film ferroelectrics, where large shifts in the Curie temperature are predicted, and there is a good agreement between theory and experiment after correcting the domain effects . In magnetic materials, the values of calculated by self-consistent fields with frozen magnons are in generally good agreement with experiment within about 20%, even for complex ternary alloys with mixed ferro- and antiferromagnetic interactions . All of these successful calculations have occurred in well-ordered crystals; methods based on ideal lattice models thus may not be equally successful for strongly disordered materials like ceramic superconductors.
2. Exotic Superexchange and TraditionalElectron-Phonon Interactions
Much of the theoretical literature over the last two decades has been devoted to discussing nonphonon models of HTSC. Did Bednorz and Mueller suppose, when they discovered HTSC in the cuprates, that they were also opening what would turn out to be a Pandora’s box for theorists? Certainly, by looking for superconductivity in a family of materials known not for metallic, but for antiferromagnetic properties, they were already behaving as contrarians, who worked evenings on this project, as they felt that this research direction would not meet with the approval of their immediate superiors. Had they consulted me, I would have asked them why they expected to find superconductivity in these pseudoperovskites. Their explanation that the strongest electron-phonon interactions are found in the best ferroelectrics (like , which has the closely related perovskite structure) would not have satisfied me. The perovskites exhibit many displacive distortions, and a would be metal should be rendered insulating by Jahn-Teller distortions.
In fact, my general argument was correct for almost all such materials, almost all, but with a few crucial exceptions() As I later learned, the crystal chemist who discovered had made a prescient remark (references for this and many other older papers can be found in my book ). He noted that was the only cuprate known at that time with an undistorted tetragonal structure. In all other cuprates the lattice planes had buckled due to strong Jahn-Teller distortions, and these same distortions would suppress metallic conductivity and of course superconductivity. No one could blame theory (or me) for not predicting the rigidity of planes, and I was off the hook for the moment, but there were much bigger challenges yet to come.
These new challenges emerged in a way that took me even more by surprise than the Bednorz-Mueller discovery. It had been known for decades that superconductivity and magnetism are incompatible, because electron-spin scattering breaks Cooper pairs. There are elaborate many-body ways of deriving this result (based on four-particle scattering diagrams called plaquettes), but the simplest way is to invoke Helmholtz’ theorem, which states that any vector field can be decomposed into complementary parts: solenoidal (magnetic) and irrotational (extensive, in other words, superconductive). This is, in fact, a “poor man’s” way of deriving the Meissner effect.
Soon phase diagrams appeared that showed that as the doping level increased, magnetism faded and superconductivity appeared, just as one would have expected. However, even before phase diagrams became available, theorists had jumped in with explanations, and the first explanation was not the most natural one, but the most surprising one, even more surprising than the discovery itself. Anderson proposed that HTSC was caused not by phonons, but by superexchange between spins(), a subject that he had discussed in 1950 for insulators. It seems that he had long hoped to find superexchange in metals, and it appeared to him that HTSC were just what he had been looking for. He termed his new mechanism “RVB” and it soon became by far his most cited paper (5000 citations so far). Anderson is still advocating RVB  and that HTSC was caused not by phonons, but by superexchange between spins(), and he has persuaded many distinguished theorists to join him . His example has stimulated many frivolous theories.
Of course, not everyone was in love with superexchange. Sir Neville Mott had always championed a common-sense approach (today known more popularly by the computer scientists’ acronym KISS), and initially he suggested that HTSC could be caused by a mixture of electron and spin interactions. However, he soon abandoned spin altogether, and turned to “bipolarons” by which he meant Cooper pairs formed by very strong and very localized electron-phonon interactions [12, 13]. However, while there is no doubt that very localized electron-phonon interactions exist at dopants (such as interstitial O) in these materials, it is not easy, especially with such large unit cells and so many normal modes, to distinguish experimentally such dopant interactions from host Jahn-Teller distortions. Indeed, even in the old intermetallic “high temperature” superconductors, with , it was often Jahn-Teller distortions (or other lattice instabilities) that had ultimately limited , while magnetic interactions, even with small amounts of magnetic impurities, quickly destroyed superconductivity. T. D. Lee also suggested that HTSC might be more like Bose-Einstein condensation, and there are still papers on HTSC using the B-E approach. In my opinion, this approach is insufficiently material-specific, and does not identify the key aspects (like the rigidity of planes) that make the cuprates special.
From the point of view of materials science, what was special about the cuprates was (and still is) that they are at the cutting edge (sometimes called the bleeding edge) of new materials: not only are they complex chemically, but also oxides per se previously enjoyed a very poor reputation among crystallographers: the samples were often oxygen-deficient, and the sample quality was often so poor that X-ray structural determinations did not meet the standards required for publication in archival diffraction journals. It seemed to me  that these problems suggested that these strongly disordered materials should be regarded as mechanically marginally stable (MMS). MMS is apparently unapproachable theoretically; the reason is that too little is known about interatomic forces, and with many atoms/(unit cell), even small errors in these will cause the dynamical matrix to produce negative values of for some and some mode . The current state of the art (2009) is that MMS in ferroelastic and ferroelectric BaTiO3 (but not ) has been solved by brute-force first-principles pseudopotential calculations. However, even the host compound is a very long way from (large lattice distortions near dopants are always ignored, as they are a large problem for brute-force approaches, but as we will see, there are other ways to deal with them).
When is calculated for HTSC using crystalline continuum metallic ( or Eliashberg) rules, not only are the predicted values too low but also the chemical trends are wrong (with some fudging of the adjustable Coulomb repulsion parameter , in may be brought close to experiment ( = 0.15, = 38 K), but the same value of in gives 1 K, a failure compared to experiment ( = 0.1, = 90 K) . The feature that distinguishes ceramic HTSC from metals is their strong disorder, as reflected in complex patterns of nanodomains on a length scale 3 nm [16, 17]. In the presence of strong disorder, superconductivity may become molecular in character [12, 13], in which case could be as high as 380 K . Unfortunately, this upper bound is too weak, and is unlikely to be reached, because in the presence of strong electron-phonon interactions the metallic band at will be split by a Jahn-Teller effect (e.g., monovalent dopants could form electrically inactive dimers); worse still, the entire compound may not be dopable, or may phase-separate.
3. Chemical Factors: Size, Apical Oxygens, Electronegativity, and Valence
A different and more global approach to the exponential complexity associated with strong disorder relies on traditional analysis of chemical factors (valid in crystals, molecules, and glasses)  to analyze trends in . Some have argued that cuprate superconductivity must be localized in the planes , but if this were the case, the maximum ’s in each material family, , would be nearly constant, much like the planar lattice constant. This is far from being the case. As one can easily see from structural systematics , the central problem in ceramic superconductors lies in making a ceramic conducting by heavy doping. Light doping (as in semiconductors) is not enough because as the ceramic dielectric constant is small, the dopant orbitals are also small, and these will not overlap unless the dopant level is high. Maximum doping levels in rigid semiconductors are typically 1%, so something special is required to support the high doping levels found in ceramic superconductors and still avoid phase separation.
In cuprates, the special factor is the exceptional rigidity of planes (see Section 2), which allows the intervening insulating layers to be soft and flexible. Because core repulsive potentials are “hard” it is then relatively easy to dope the soft insulating layers. Note that normally one thinks of metals as soft, and ionic insulators as hard. The cuprates and a few other layered ceramics reverse the normal ordering, and this is what makes it possible for them to be HTSC. There are no mysterious superexchange interactions between spins; most of the antiferromagnetic regions have disappeared by the time the doping is large enough for the materials to be metallic. The pseudogaps are still present, and they play a necessary role, but whether or not they are caused by magnetic interactions (unlikely) or charge density waves (or Jahn-Teller distortions) (probably) is incidental. The highest , reached at optimal doping in a given alloy will depend on the dopant configuration relative to the regions occupied by the pseudogaps. That, in turn, will depend on the relative sizes of the ions, a packing (actually, a dynamical packing) question that is well beyond the reach of present and probably any future theory. As we will see in the following section, with a sufficiently large data base this difficulty can be handled by advanced statistical methods.
Kamimura recognized that the planes alone could not explain HTSC, no matter how exotic the interactions within them, and he suggested that apical oxygens could play an important role ; several succeeding “apical oxygen” papers also proved quite popular [22, 23]. There have always been strong indications that apical oxygens are coupled to interlayer dopants (especially interstitial oxygen, which is close to apical oxygens and can form dynamical vibrational bands with them) based on chemical trends between apical oxygen bond lengths, ordering and , and we will see further evidence of such correlations later. However, specific apical oxygen models always introduced atomic orbitals and their overlaps, which generates many parameters to fit one observable, a situation that always leads to “excellent” agreement between “predicted” and experimental values. In fact, the most popular model  is based on the difference between the Madelung potentials at the planar and apical oxygen sites, calculated with an artistic point ion model where most of the many charges in the unit cell are freely “assigned” (e.g., although O is usually 2, in some cases it is “assigned” a charge of 1, and many liberties are taken with “assigned” cationic charges). A parameterized discussion of correlations between apical oxygen bond lengths and  gave plausible trends, but it covered only a few cases with no predictions of , showing the limitations of as a configuration coordinate. More generally, one should not use extensively parameterized atomic models ( planes apical oxygens) to discuss differences between pseudogapped regions and superconductive regions, as this difference is almost surely due to different dopant distributions .
When one considers seven different structural factors, including apical oxygen bond lengths, and correlates them with , one finds that the obvious ionic variable, the average over all host atoms of the difference between cation and anion electronegativities , gives the best fit to . (This is the ionic analogue of the covalent molecular model .) Bearing in mind that different dynamical packings can be used to maximize , we can now test the validity of as a coupling parameter by plotting . The results are quite disappointing, as they yield a scatter-shot plot , which means that the traditional chemical approach is too simple to explain HTSC (the reason is that to produce a strong electron-phonon interaction, we need a soft lattice, and soft lattices will be found near a covalent-ionic-metallic triple point, which will not depend on alone). It is just at this point, when nothing seems to work, that we can find the answer, using only the elements discussed so far.
4. Successful Prediction of
We begin by realizing that volume factors although they are not known in detail, can be included implicitly in the analysis by focusing initially not on , but rather on the largest transition temperatures , where is any other chemical factor. In other words, if the volume factor has already been optimized, then the material in question will have = . For those familiar with Bayesian probability, this approach is readily recognized: Bayesian probability interprets the concept of probability as a contingent “measure of a state of knowledge” and not as a frequency in orthodox statistics (further details can be found from your browser). Bayesian methods can be extremely effective, but the Bayesian filter requires a large data base. In what follows, the basic Bayesian conclusions are tested by employing the full ceramic HTSC data base, which has now grown quite large, including ceramics based on metallic layers other than planes and apical ions other than oxygen.
At this point there are only two chemical configuration coordinates remaining: electron/atom (e/a) ratio (which determines the Fermi line of a two-dimensional metal), and valence, which apparently is relevant for perovskites and pseudoperovskites, where the average coordination number is far lower than in metals. In a continuum model the e/a ratio would be the relevant one, while in a valence bond network model valence is the key coordinate; this coordinate can compete with structural coordination numbers . The latter are much the same for most cuprates, and are unlikely candidates for . Moreover, decades of research on a parallel problem, network glasses, have shown (particularly when comparing silicate and chalcogenide alloy glasses) that the MMS of such densely packed glasses (which permits them to avoid crystallization) depends primarily on the number of Pauling resonating valence bonds (e.g., in NaCl there is one Pauling resonating valence bond/ion, although the coordination numbers are six) . The value of for Cu in the cuprates is 2. There are similarly obvious rules for for other elements (including those with mixed valence, Tl, 1,3, and Bi, 3,5) , and of course, (O) = 2, while e/a(O) = 6. The conclusion (also taking into account many results for network glasses) is that while is a good coordinate for ionic and covalent molecules, it is a very accurate configuration coordinate for strongly disordered networks, even in the presence of lone pair interactions . The valence bonds that one is counting determine the MMS of the network, while the dopants provide the metallic carriers. Of course, in metallic superconductors, e/a is the relevant chemical factor, so by replacing e/a with we have not only identified the central difference between metallic and ceramic superconductivity, but we have done so quantitatively.
5. MMS and Coarse Graining
The question remains of how valence or is to be averaged over the many atoms in the unit cell: should the rigid metallic planes be weighted more heavily, or the soft layers between them, where the dopants are. Again decades of research on network glasses have shown that the best weighting is the simplest, that is, equal weighting for all atoms provides the best description of glass-forming ability and the glass transition, because the overall network is mechanically marginally stable (MMS). As discussed earlier, shell-model calculations  of phonon spectra in HTSC are generally unable to predict very soft modes, especially those associated with dopants. Quite revealing is the fact that the fitted effective charges for “soft layer” rare earth cations in shell models of LSCO and YBCO phonon spectra derived from neutron scattering were inexplicably negative . Neutron scattering has successfully identified Jahn-Teller distortions associated with high-frequency optical modes, and these set the overall scale  for , but it is unable to resolve very soft modes .
Although MMS is concealed from experiment and theory in HTSC, the simple and universal assumption of equal weighting of all atoms is fully effective. In retrospect, it is easy to see why equal weighting works so well. HTSC exhibits nanodomains spanning 10 unit cells [16, 17], so the soft modes implied by MMS are spread not only over a single unit cell, but in fact over many unit cells (coarse graining), all of which are sufficiently disordered by dopants and pseudogap instabilities that equal weighting within a unit cell becomes almost as accurate as in fully homogeneous network glasses.
Guided by these considerations, which are general, specific, simple, and free of adjustable parameters, we plotted , with the results shown in Figure 3. It is important to understand how the predictive dotted line was drawn. First, note that all the HTSC with are well known, and in fact were discovered chronologically with decreasing , starting with (a cubic perovskite, with a phase diagram quite different from the cuprates, and only hints of an emerging nanodomain structure , but it still fits nicely on the smooth dotted line). Secondly, if one knows only the ascending curve for 2, one might reasonably extrapolate it to very large for 2. When the predictive dotted line was drawn initially, only one point was known for that for the oxyhalide NCCOC() with Na (not O) dopants, an apical Cl (not O) and K. There is no phenomenological reason to suppose that this value of represents a realization of , that is, that K = . Nevertheless, one can note that (NCCOC) is approximately the mirror image of (LSCO) about = 2, so on the basis of percolative symmetry it seemed natural to draw the predictive line as shown. Later, (apical F) was reported to have = 55 K, which is comfortably below = 78 K on the predicted line, so this point was added to the published Figure  as its first “predictive” success, assuming that this value still did not represent a realization of . Finally postdated improved sample preparation  gave (BCCOF) = 76 K, reducing the discrepancy between the predicted value of and experimental value of for BCCOF from 23 K to 2 K. This is a very convincing second (and predated) predictive theoretical success, especially considering that neither NCCOC nor BCCOF contain apical O, which means that the homology is unexpectedly general. Of course, further large increases in (NCCOC or BCCOF) by 20 K would be sufficient to falsify the theory, although even then it would be better than the only available alternatives which predict higher by as much as 200 K.
The analysis given here is based on minimal logical and statistical considerations, but the results were actually derived from a physical model that the author first proposed 20 years ago . The zigzag self-organized percolative model (ZZIP) has many attractive features: for instance, the energy scale for , which is merely set empirically in Figure 3, is apparently set for 2 by the Jahn-Teller shift in the (100) LO phonon energy (there are no oxyhalide data for 2), as shown by Figure (b) in , which suggests a close dopant-mediated relation between the soft acoustic and optic modes. Substantial evidence shows that percolative filaments are formed at high temperatures and account for many features of transport up to at least 300 K . At present there exists no alternative model that can predict in HTSC.
6. Cuprate-Like Superconductivity
There are several new marginally stable families of layered crystals that exhibit many similarities to the cuprates: there are many atoms per unit cell, with displacive lattice instabilities, vicinal antiferromagnetic phases, and so forth, including ionic ZrNCl  and the rapidly growing covalent superfamily based on FeAs, such as LaFeAs . Are these similarities accidental, or can the percolative cuprate ionic superfamily model explain HTSC in these noncuprate-layered materials with no additional assumptions? In fact, the percolative model easily explains the similarities, by bringing these new materials into the general framework of self-organized networks. This has already been done for ionic (Zr,Hf)NCl ( K–25 K) , so now a similar discussion is given here for the covalent LaFeAs superfamily ( K–43 K) , which is much larger and the subject of hundreds of recent studies.
Because these materials are mechanically only marginally stable, they are strongly disordered when doped, and are generally far from optimized with respect to HTSC. Marginal lattice stability determines the overall scale for , as the phonon energy shift measured by neutron scattering associated with Jahn-Teller doubling of the unit cell of LO phonons correlates linearly with in the cuprates ; of course, spin and antiferromagnetic exchange show no such scaling, and are irrelevant. The least upper bound for , called , has a strongly percolative character, as it peaks exponentially at = 2, where is the average valence number of all the atoms [28, 30].
The master function is shown in Figure 2 for the cuprates; the peak at = 2 has a cut-off exponential character. The point for ionic HfNCl was discussed previously , and we now discuss the points for the LaFeAs family ( K–43 K). Here = 2, just as for Cu, because is in a 2+ valence state [39, 40] in a virtual crystal model. This band model also shows the beginnings of self-organization, in that the average height of is found to shift with ; had the calculation been carried out with a large supercell centered on an dopant?, would have varied with distance from . This virtual crystal relaxation effect alone shows that N varies slowly and smoothly with doping (which means that the apparent Fermi planar line becomes very broad near a critical point), and hence effective medium models cannot explain HTSC. However, from this one should not conclude that electron-phonon interactions do not cause HTSC, as these interactions (not superexchange) do set the overall energy scale  through Jahn-Teller distortions on and near percolative paths, and these distortions are especially large near dopants.
When one calculates for undoped LaFeAsO, one obtains = 2.5, which places ( = 26K) very close to LixZrNCl on the master curve of Figure 2, so that the theory appears to succeed effortlessly. However, is maximized at 43 K for pressures near 4 GPA , an increase of 60%, which is much more than is seen in cuprates, and exceeds the upper bound of the master curve. Does this falsify the theory? No, because the equilibrium cuprate master function remains valid for the ZrNCl and families, but the pressure dependence in the latter family is larger than in the cuprates, as Fe-As bonding is more covalent than largely ionic Cu–O bonding , due to the larger Pauling electronegativity X differences ( = 1.8, = 2.0, = 1.9, = 3.5)) in the cuprates. Covalent bonding also seems to limit the range of for which stable crystals can form; thus the smallest value of for the FeAs family seems to be near 2.3 in () .
It is striking that this covalent FeAs stability range of 2.3 2.5 is very similar to the range 2.25 2.52 for stress-free covalent glasses previously shown [28, 30] in Figure 2. (Again this is a rather remarkably successful predated prediction.) Thus the covalent instabilities of the host lattice, especially the reduced rigidity of the FeAs plane relative to the plane, are the factor that shifts the value of at which peaks from = 2.0 in the ionic cuprates to = 2.5 in the LaFeAs family. In both cases,
so that the average connectivity of the undoped insulating plane is matched to that of the metallic plane. Apparently this hidden topological layer symmetry (1) determines the maximum electron-phonon interactions in marginally stable layered pseudoperovskites.
7. Surfaces and Interfaces
The percolative master function is determined from bulk data on layered crystals, so one can ask whether or not this function can explain trends in at surfaces and layer interfaces. Determining at surfaces and interfaces is much more difficult than in the bulk, where it is natural to average over all atoms, as the self-organized structure is marginally stable overall, and soft modes that are critically bound to percolative superconductive paths should have long wave lengths, as is still small compared to the melting temperature. However, in layered thin crystalline films with epitaxial interfaces or in clusters at doped free surfaces, similar percolative behavior is expected. This turns out to be the case for the – ( = 0.45) interface, where K, after enhancement by exposure to ozone from 30 K . The giant ozone enhancement is readily explained by the addition of oxygen dopants, absorbed by to give with . However, the maximum obtainable in this way is 30 K for both layers separately, apparently producing a mystery.
Let us look at this mystery with the master curve: = 16/7 in LCO = 2.28, = in = , so with (or ) = 0.15, = 2.26, and with = 0.45, = 2.22. This would give a decrease in between = 0.15 and = 0.45 of 0.04, and so we get something like = 35 K + (0.04/0.28) () K = 50 K. Of course, this is just a plausible guess at the interfacial structure, but the master function has given the trend correctly, not only qualitatively but also semiquantitatively (something no other theory has been able to do: virtual crystal theories predict 1 K, from which it has often been erroneously concluded that electron–phonon interactions do not cause HTSC).
Now we turn to a much more difficult problem, for which the data base is small, but still robust: a surface monolayer of , where is an alkali metal (Na  or Cs). While bulk exhibits superconductivity only near 1 K, here for Na superconductivity appears around 100 K; for Cs there are two phase transitions, a bulk one with lower at higher doping, and a re-entrant percolative one with higher at lower doping. Moreover, Na– and Li– (but not K–) doped surfaces of nanoclusters of embedded in a variety of nanoporous hosts (carbon inverse opal, carbon nanotube paper, or platinum sponge) show diamagnetic anomalies with an onset of 130 K . Note that (with its simpler unit cell, subject only to Jahn-Teller distortions) itself is nonmagnetic, as is another HTSC(BKBO, (Ba,K)).
These data can be combined with the master function to construct a model of percolative self-organization at surfaces. In bulk the valence of is 6, and = 3.0, far to the right on the master function , where (3) 5 K. Near the surface the valence of could be 2 (just as with Cu in the cuprates, and Fe in the FeAs compounds). To explain K, one must assume = 2. A percolative O surface chain then has = 2. These surface chains are entropically broken into stress-relieving fragments. Intercalated Li or Na ions connect the chain fragments, thereby increasing their conductivity and their screening of internal ionic fields, just as in the bulk percolative model. The embedded clusters are not connected, so the result is “localized nonpercolative superconductivity” still with = 2 . In the free surface case [45, 46], thermal fluctuations disrupt superconductivity above 100 K. Both of these = 2 points are shown in Figure 2. Considering the rapid progress in nanoscience, it may be possible to obtain similar pairs of percolative and cluster points for other HTSC.
Finally, self-organized percolation enables us to understand how cointercalation of organic molecules M with Li in ionic can uniformly enhance by up to 30%, over a wide range 0.15 0.50, even though the average interlayer spacing varies by as much as 30% . The intercalated organic molecules reduce the dielectric screening of Li–centered electron-phonon interactions by other Li ions. Note that the nominal concentration of the Li ions may refer only to patches that strongly diffract; the superconductive paths may pass through patches with a concentration different from , explaining why is apparently constant over a wide range of . Only a few percolative paths are required to exclude Abrikosov vortices and produce HTSC; this is why often increases when the average density of states N() decreases (e.g., in the cuprates compared to the covalent FeAs family, or the ionic family ). This is yet another example of the paradoxes generated by attempting to understand a self-organized percolative phase in terms of continuum concepts such as Bloch-wave Fermi surfaces, modulation doping, or plasmon waves. Note that these points have often been made in earlier papers on the topological percolative model, long before any of these new materials were discovered.
8. Mapping ZZI Percolative Paths
For most of the last two decades experiment has provided largely circumstantial support for the zigzag interlayer percolative (ZZIP) network model shown in Figure 4, but recently more direct evidence has appeared. The model has two key elements: the dopants, often interstitial oxygen, whose positions are not easily determined, and the zigzag network paths themselves. The zigzag network paths are associated with strong electron-phonon interactions, which are especially strong for interlayer displacements. This has enabled the zig and the zag of the paths to be identified by a spectacular combination of time-resolved electron diffraction , for the -axis zag component of the paths, and anisotropically strong kinks in quasiparticle dispersion observed by angle-resolved photoemission , for the ab planar zig component of the paths. The data show that the -axis Cu-O zag component has faster dynamics when the femtosecond pulse probe is polarized along the planar Cu–O zig component, to which it can be coupled through planar Cu–O bond buckling. It is difficult to understand these correlations unless the -axis zag component is actually topologically connected to the planar zig component. One might argue that such a connection occurs only at low temperatures, and would be ineffective at the high excitation energies of the electron diffraction experiment, but this is not correct. High-temperature transport data show that the self-organization (hard wiring) of the ZZIP network begins already at annealing temperatures ; the results are fully consistent with the zigzag network model discussed in dozens of papers over the last 20 years. There remains one puzzling aspect: anisotropy is observed in both Bi2212 and Bi2223 by ARPES, but only in the former by electron diffraction. The extra layer in the latter would not appear to erase the planar anisotropy, but it is possible that Bi2223 has a high density of stacking faults. Depending on the geometry of the percolative paths, such faults could erase the observed anisotropy by scattering percolative carriers.
While we are on the subject of percolation versus continuum models, it is important to realize that while the presence of self-organized percolative paths introduces exponential complexity into the Bohmian wave-packet basis states  used to form Cooper pairs, it in no way alters the nature of the attractive electron-phonon interactions responsible for forming the pairs. These two points have often been confused, and the failure of continuum plane wave basis states to describe cuprate HTSC has often been used to argue that electron-phonon interactions do not cause HTSC . Because the fraction of carriers involved in percolative paths is small, many negative indications of strong electron-phonon coupling have been found; for example, bulk phonon softening is so small as to be unobservable by neutron scattering at high energies . Therefore it is gratifying that quasiparticle tunneling across a break junction perpendicular to the superconducting copper oxide planes showed 11 phonon features that match precisely with Raman spectra , decisively showing that HTSC is indeed caused by electron-phonon interactions along the -axis, as previously argued from dynamical relaxation experiments . Also the long-expected isotope effect at the phonon kink has been observed by ARPES . The fact that all the -axis phonon bands appear in the break junction experiment, and not just those associated with the O buckling mode in the plane , strongly supports the present model of zigzag percolative paths in a marginally stable all-atom network. Finally, it is worth stressing that the phonon features that correlate by far the best with are exactly those of the atoms in the soft insulating layer [56, Figures 11 and 12], as assumed in the zigzag model, and not the atoms in the rigid layer, as is often wrongly assumed .
There is one interesting aspect of the original 1989 ZZIP model that was confirmed experimentally by anomalous X-ray diffraction , but the significance of the data was not realized because they were not connected to the theoretical model. Namely, in the model the metallic layer nanodomains are staggered, as this facilitates the construction of filamentary paths that pass through dopants in the nonmetallic layers. The data showed that “in each bilayer the flat stripes in a first layer are close to the bent stripes in the second layer” from which it was concluded that such a staggered structure “suppresses the electronic coupling between the two adjacent planes”. In the ZZIP model just the opposite is true: the nanodomains are staggered in order to increase the electronic coupling between the two adjacent planes, and this is part of the self-organization of the “hard-wired” filamentary network that is formed at high temperatures (above 300 K), as shown by many normal-state transport anomalies, notably the linearity in of the planar resistivity , compared to the dependence characteristic of a Fermi liquid. Of course, in a one-dimensional filament, intrafilamentary scattering always gives such a linear dependence.
A few comments are in order regarding the parabolic form of . This starts for small when the percolation threshold is reached, and it ends for large when all the isolated percolative paths have lost their separate identities and become metallic bundles. At and above = continuum theory becomes valid, and it immediately shows that for is either very small or zero. The reason for this is simple: the charge density is so low that Coulomb repulsive interactions outweigh attractive electron-phonon interactions, just as they do in metals like Na and Cu itself.
9. Single-Layer Cuprates: MechanicallyMarginally Unstable (MMU)
The importance of self-organized percolative paths is nicely brought out by the single-layer compound Hg , which has = 2. This compound has the largest = 95 K of any single-layer cuprate, but it does not appear in our figures because it is isovalent to HBCO(Hg), which also has = 2 and = = 135 K. There are several interesting aspects to HgBa2CuO4+δ: the Cu–O bond lengths (including the apical O) are expanded by the Ba ions (which act as spacers), and the soft Hg layer is strongly disordered (as expected in the zigzag model). If superconductivity were confined to the layer  and the apical O [22, 23], this expansion should have greatly depressed (because of strengthened Coulomb or ionic interactions), but the contrary occurred. In the 1989 zigzag model  the layer functions as an electrical connector, while the strong e-p interactions occur in the soft, strongly disordered Hg layer, so the relatively large = 95 K is a natural feature of the model. The coupling of HTSC to lattice disorder (not order) is directly and elegantly shown in . Superconductive formation and overlap of zigzag percolative filamentary arrays can increase lattice disorder. When the layers were under compressive strain (so that the critical axial zag paths were under tensile strain, and thus more flexible), this is what was observed as decreased well below , where the superconductive energy is largest. Very similar effects appear in the FeAs family as well ; a more extensive percolative discussion will be given elsewhere.
None of the single-layer cuprates produces a for any . However, the single-layer cuprates form an interesting homology family in their own right; in contrast to Section 5, they can be described as mechanically marginally unstable (MMU). Theorists have long known that individual planes readily buckle. When this happens in the cuprates, the pseudogap charge density wave regions expand, the metallic regions contract, and (the density of superconductive carriers) rapidly drops, and with it . Thus another factor comes into play, to stabilize the overall MMU network, and retain larger metallic regions. This factor is the purely ionic static Madelung potential (the rigid ion model omits polarization or screening energies, which are important dynamically, but less important statically) . Within the restricted context of single-layer cuprates only, it appears that it is this factor that dominates . Note, however, that the single-layer cuprate family never contributes to , and therefore this family should be regarded as nonoptimally packed ceramic superconductors (and, therefore, more in need of stabilization). Moreover, the stabilizing space-filling (buttressing) effect of the large Ba ions in Hg is not accounted for by the Madelung potential, and here lies well above the Madelung trend line for the other single-layer cuprates . This is further evidence that the single-layer MMU cuprates form a different homology family from the multilayer MMS family.
Among the (relatively) low ceramic superconductors, has attracted much interest because here it appears that the pseudogap and superconductive gap are best separated [61, 62] relative to other micaceous multilayer cuprates. The reason for this is clear: not only is this material MMU, but also the stabilizing ionic factors are weak, reducing the density of superconductive filaments and filament-filament interactions, and producing a more homogeneous superconductive gap that is well separated from a much larger pseudogap.
What else can we learn from the single-layer cuprate MMU family? is a member of this family, and it also falls on the master function of MMS superconductors, and so is also an optimally packed ceramic zigzag percolative superconductor. Which factor (MMS or MMU) is more important at the interface? In the MMU case, we know that the Madelung potential that stabilizes planes decreases as x increases, in accordance with the fact that=0 ( = 0.45). However, the Madelung potential at the – ( = 0.45) interface can be estimated to be that of (=0.22), so that should have decreased from 38 K at to 30 K. In fact, increased from 30 K to 50 K, which is what the master function of MMS superconductors predicts (Section 7). At optimized interfaces, percolative effects dominate, which is what happened with surface layers (Section 7).
The present review shows that the original ZZIP model [35, Figure 4] continues to provide an excellent universal guide to the phenomenology of ceramic superconductors. Initially, it explained the large qualitative differences between HTSC in cubic and layered ceramics (Figure 1). It is the only theoretical model so far that has been able predatively to predict (BCCOF) 75 K, but it also quantitatively predicts superconductive , even for noncuprate HTSC, starting only from the cuprates, which no other theoretical model has done. The self-organized marginally stable percolative model unexpectedly transcends conventional chemistry (the materials covered include cuprates, tungstates, zirconates, ferrics, arsenides, bismates, oxides, halides, Li–, Na–, Cs–, O–, F–, Cl–doped, and the structures include bulk, interface, and nanocluster surfaces); so far as I know, there is no other example in solid phase transitions where theory of any kind (continuum or otherwise) can predict transition temperatures with such universal success. The results make an overwhelming case for a new homology class of glassy network doped superconductors, separate and distinct from continuum metallic superconductors.
As noted previously , the theory predicts with an accuracy of 10 K, compared to a melting point of order K, which is an accuracy of 1%. However, this success contains a subtle aspect, which is that because HTSC is concerned with marginally stable lattices, it is important to build this theoretical mechanism into the analysis from the outset (Section 4). This has been done by mapping , and examining different choices of : only = gives the apparently exponentially resonant peak that is strongly suggestive of percolation.
The theoretical debates stimulated by HTSC have lasted for more than 20 years, and have often severely tried the patience of the physics community. Were they worth it? I believe they were and still are. The basic issue was, and still is, whether it is legitimate to treat a discrete, exponentially complex problem involving strongly disordered, self-organized materials, at the cutting edge of materials science, with the same simplistic continuum methods (including polynomial Hamiltonian algebra and/or Landau order parameters) that students have learned work so well for toy models and some simple crystalline solids. The experimental evidence strongly suggests that this discrete, exponentially complex problem can be solved by focusing on its essential topological features, derived from the network structures of ceramic HTSC .
Global topology is still something of an oddity among mathematical disciplines (it is very young, dating from 1877). It is standard among computer scientists, but it is unfamiliar to most chemists and physicists. It is ideally suited to treat complexity problems, including many far afield from science, such as economics [63, 64] and difficult problems in biology, such as the network of protein-protein interactions ; for pioneering research in NPC computer algorithms addressing exponential complexity . M. Karp was awarded the 2008 Kyoto Prize. It also transcends the otherwise theoretically insuperable barriers of exponentially complex (NPC, nonpolynomial complete), aperiodic self-organization commonly encountered not only in HTSC but also in protein science [66, 67]. From sandpiles to proteins, it appears that the best documented examples of self-organized criticality (SOC) are found in network glasses  and HTSC .
The (by now very old) debate over whether HTSC is caused by conventional electron–phonon interactions, or by exotic electron-spin interactions, continues even for the cuprates  although it would appear from Raman scattering experiments to have been settled conclusively in favor of phonons [53, 56, 70]. In particular, infrared optical spectra  contain a mixture of overlapping superconductive and pseudogap (or Jahn-Teller) features that are not easily separated, even in optimally doped samples. As the infrared spectra are dominated by electric dipole transitions, it is difficult to believe that any of the “coincidences” between isolated neutron magnetic resonances and fictive single optical resonances used to fit  these entangled gap spectra are significant, especially as results internally consistent with gap phase diagrams measured by other methods do not appear to have been obtained for underdoped and optimally doped phases. Simpler and better polaronic fits show no correlations between midinfrared peak positions and .
These infrared data merely reinforce the large qualitative difference between layered ceramics and cubic shown also in the phase diagrams of Figure 1; the latter has a normal BCS-type infrared spectrum with /k = 3.2() . There have been many studies of the metal-insulator transition at in and these have been interpreted in terms of bipolaron formation . However, a more appealing interpretation of the metal-insulator transition would be the onset of percolative metallic patches, as the “bipolaronic” infrared dopant peak appears to merge with the CDW band edge at , where is largest. In other words, the two lattice deformations merge to form nonfilamentary continuum superconductive metallic regions in a first order metal-insulator transition.
Application of “first principle” continuum theories to the FeAs family has uniformly led to the conclusion that electron-phonon interactions cannot cause HTSC in this family [39–41, 74, 75]; similar conclusions were reached earlier for the cuprates . The correct conclusion is that continuum (ideal lattice) approximations are invalid because of strong disorder and nanoscale phase separation [76–78], as well as the much more subtle exponentially complex consequences of zigzag self-organized percolation, ZZIP (Section 8). The combination of electron-phonon interactions and ionicity readily explains  how superconductivity in the covalent (noncentral interatomic forces) FeAs family can be much more isotropic than in the cuprates , yet still retain a lowered dimensionality. Strong disorder explains “hump-dip” pseudogap tunneling features in terms of charge density waves .
Probably the most accurate ceramic HTSC phase diagrams are those obtained by studying the planar resistivity , which is most linear in at and near optimal doping [30, 82]. The dopant network-forming interactions, although individually weak, are cumulatively very strong because the dielectric energy gained by screening internal electric fields increases as the network conductivity increases due to dopant self-organization. The maximization of the -linearity of near optimal doping [30, 82] was the first normal-state transport anomaly to be discovered, but in the intervening 20 years theory has been unable to derive this maximization, and it seems unlikely that this extremal will ever be derived using conventional polynomial methods (e.g., Landau Fermi liquid theory predicts a dependence). This situation is typical of exponentially complex problems which are characteristic of networks, but it can be repaired by carefully designed experiments.
In ceramic HTSC self-organization effects manifest themselves by a sharpening of properties characteristic of networks. An obvious and trivial example of such sharpening is the narrowing of the superconductive transition itself, which can be promoted by annealing; this is a small effect for traditional metallic superconductors, but a large effect in ceramic HTSC. If the maximization of the -linearity of near optimal doping is indeed caused by network self-organization, then that should be manifested by an increase in -linearity upon annealing. Studies of redistribution of oxygen at a fixed oxygen content in the chain layers of slightly underdoped YBCO with a nonlinear showed  that annealing for 2–8 hours at 400–420 K does lead to an increase of by about 1 K and a reduction of the nonlinear component in by 10–15% just above .
The classic work of  has recently been extended to high magnetic fields well above , with spectacular results . It is found that the regime which is most linear in occurs in at (), and that this linear regime extends at fixed vertically all the way from = 0 right up to the highest studied (200 K). This result is inexplicable if one thinks of = as a “quantum critical point,” but it is perfectly understandable in the context of a hard-wired ZZIP network, formed at the annealing temperature . In fact, one can go further: the vertical linear regime is shaped like an hour glass, wide at = 0 and = 200 K, and narrow at 100 K. This narrowing is due to the formation of pseudogap islands, which requires a reformation of the nanodomain network at low , into a doubly percolative network, with two kinds of dopants .
Naturally, percolative conductive paths are phase-sensitive, and when this aspect is combined with the effects of long-range conductive screening of internal electric fields, it is easier to understand why descriptions of disorder using functions dependent on amplitudes alone (such as the participation ratio) are insufficient to describe filamentary self-organization . Finally, it is worth mentioning that the philosophy employed here in the search for a satisfactory percolative solution to this exponentially complex glassy network problem  can be justified (after the fact of its success) not only heuristically but also by formal Boolean algebra . This algebra shows that the determining factor in fixing the properties of exponentially complex systems is their topology, not their geometry [87, 88]. Of course, topology is a characteristic feature of networks, especially in strongly disordered layered structures, that is absent from continuum (ideal lattice) models.
I am grateful to Professor T. H. Geballe for stimulating my interest in MMU ceramic cuprate superconductors.
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