inferring planar disorder in close-packed structures via...

Acta Crystallographica Section AFoundations ofCrystallographyISSN 0108-7673

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Inferring planar disorder in close-packed structures via!-machine spectral reconstruction theory: examplesfrom simulated diffraction spectraD. P. Varn,a,b,c*†G. S. Canrightc,d* and J. P. Crutchfield a,b*‡aComplexity Sciences Center & Physics Department, University of California, Davis, One Shields Avenue,Davis, California 95616, USA, bSanta Fe Institute, 1399 Hyde Park Road, Santa Fe, New Mexico 87501,USA, cDepartment of Physics and Astronomy, University of Tennessee, 1408 Circle Drive, Knoxville, Ten-nessee 37996, USA, and dTelenor Research and Development, 1331 Fornebu, Oslo, Norway. Correspon-dence e-mail: [email protected], [email protected], [email protected]

Previously we detailed a novel algorithm, !-machine spectral reconstruction the-ory (!MSR), that infers pattern and disorder in planar-faulted, close-packed struc-tures directly from X-ray diffraction patterns [Varn, et. al., (2013) Acta Crystal-lographica A]. Here we apply !MSR to simulated diffraction patterns from fourclose-packed crystals. We find that for stacking structures with a memory lengthof three or less, !MSR reproduces the statistics of the stacking structure; the resultbeing in the form of a directed graph called an !-machine. For stacking struc-tures with a memory length larger than three, !MSR returns a model that capturesmany important features of the original stacking structure. These include multi-ple stacking faults and multiple crystal structures. Further, we find that !MSR isable to discover stacking structure in even highly disordered crystals. In order toaddress issues concerning the long range order observed in many classes of lay-ered materials, we define several length parameters calculable from the !-machineand discuss their relevance.

Keywords: X-ray diffraction; diffuse scattering; one-dimensional disorder; polytypes;planar faults; computational mechanics.

1. Introduction

While crystallography has historically focused on the charac-terization of materials whose constituent parts are arranged inan orderly fashion, researchers have become increasingly inter-ested in materials that display varying amounts of disorder, sev-eral examples being glasses, aerogels (Erenburg et al., 2005)and amorphous metal oxides (Bataronov et al., 2004). A broadrange of layered materials called polytypes often show con-siderable disorder along the stacking direction and have beenthe subject of numerous theoretical and experimental investi-gations (Jagodzinski, 1949; Pandey & Krishna, 1982; Trigu-nayat, 1991; Sebastian & Krishna, 1994). Polytypism is thephenomenon in which a three-dimensional solid is built up bythe stacking of identical (or nearly identical)1 two-dimensionalmodular units (Price, 1983; Ferraris et al., 2008), which wewill refer to as modular layers (MLs). Each ML is itself crys-talline and the only disorder comes from how adjacent MLs arestacked. Typically energetic considerations restrict the numberof ways two MLs can be stacked to a usually small set of orien-tations. Thus, the specification of a disordered polytype reducesto giving the one-dimensional list of the sequence of MLs calledthe stacking sequence.

Polytypes have attracted so much interest in part due to themultiple crystalline stacking sequences commonly observed—

for two of the most polytypic materials, ZnS and SiC,there are 185 and 250 known periodic stacking structuresrespectively (Mardix, 1986; Nasir et al., 2012). Some ofthese crystalline structures have unit cells extending over 100MLs (Sebastian & Krishna, 1994). This is in contrast to the cal-culated inter-ML interaction range of ! 1 ML in ZnS (Engel &Needs, 1990) and ! 3 MLs in SiC (Cheng et al., 1987; Chenget al., 1988; Shaw & Heine, 1990; Cheng et al., 1990). Animportant ancillary question is whether the disordered poly-types so commonly observed in annealed and as-grown crystalsalso possess coordination in the stacking of MLs over such along range. Additionally, SiC has received considerable atten-tion recently as a promising candidate for use as nanowiresin advanced electronics devices (Wang et al., 2011; Melinonet al., 2007). The electronic properties of SiC are dependent onboth the polytype and the degree of disorder present.

Significant simplifications in the analysis of X-ray diffractionpatterns (DPs) occur if the disorder in the crystal is restricted toone dimension and the constituent parts can assume only dis-crete positions. This is just the case that arises in the analy-sis of polytypes. While the general problem of inverting DPsto obtain structure remains unsolved, this more restricted one-dimensional case has been much more amenable to theoreticalanalysis. We recently introduced a novel inference algorithm, !-

†Correspondence Author‡Correspondence Author

1 See Trigunayat (1991) for a discussion of materials that have some variation in either the structure or stoichometry of the composite layers. In this present study,we will assume that the composite layers are identical.

Acta Cryst. (0000). A00, 000000 Varn, Canright & Crutchfield · !MSR - Simulation Studies 1

machine spectral reconstruction theory (!MSR or “emissary”)and applied it to the problem of inferring planar disorder fromDPs for the special case of close-packed structures (CPSs) (Varnet al., 2002; Varn et al., 2013).2 Although we do not find theparticular stacking sequence that generated the experimentalDP, we do find a unique, statistical expression for an ensem-ble of stacking sequences each of which could have producedthe observed DP. This statistical description comes in the com-pact form of an !-machine (Crutchfield & Young, 1989; Shalizi& Crutchfield, 2001).

We claim in a companion paper (Varn et al., 2013) that !MSRhas many significant features, including the following: (i) !MSRdoes not assume any underlying crystal structure, nor does itrequire one to postulate a priori any particular candidate fault-ing structures. That is, there need not be any ‘parent’ crystalstructure into which some preselected faulting is introduced. (ii)Consequently, !MSR can model specimens with multiple crys-tal or fault structures. (iii) Since !MSR doesn’t require a parentcrystal structure, it can detect and quantify stacking structurein samples with even highly disordered stacking sequences. (iv)!MSR uses all of the information available from the DP, bothBragg and diffuse scattering. (v) !MSR results in a minimal andunique description of the stacking structure in the form of an!-machine. From knowledge of the !-machine, insight into thespacial organization of the stacking structure is possible. (vi)Parameters of physical interest, such as entropy density, hexag-onality and memory length, are directly calculable from the !-machine.

Our purpose here is four-fold: (i) We wish to validate theabove assertions concerning the efficacy of !MSR by demon-strating its application to the discovery of pattern and disor-der in layered materials from their DPs. (ii) As developed inVarn et al. (2013), !MSR can reconstruct processes up to 3 rd-order Markovian. We wish to test the robustness of !MSR byanalyzing DPs from stacking sequences not describable as 3 rd-order Markovian. While we expect that !MSR will not recoverthe precise statistics of the original stacking sequence for thesecomplicated stacking processes, we wish to understand howmuch it deviates in these cases. (iii) We wish to address theissue of long range order in disordered polytypes. Thus, we alsodefine length parameters calculable from the !-machine and dis-cuss their implication for finding long range order in polytypes.(iv) Lastly, we wish to demonstrate how the architecture of the!-machine provides an intuitive and quantitative understandinginto the spatial organization of layered CPSs.

These goals are convincingly realized by analyzing DPsderived from simulated stacking sequences where there areno issues concerning experimental error. We are able to com-pare the !-machine reconstructed from DPs with the !-machinethat describes the original stacking structure and, thus, we canexplore how effectively !MSR captures the statistics of thesecomplicated stacking structures. Additionally, this kind of anal-ysis also allows us to identify possible difficulties that may arisewhen applying !MSR.

This present paper continues the discussion developed inVarn et al., (2013), and readers desiring to fully grasp the detailsof the examples worked here are urged to consult that paperbefore continuing. Our development is organized as follows: in§2 we provide numerical details about the techniques we use toanalyze the simulated DPs; in §3 we present our analysis of foursimulated DPs using !MSR; in §4 we define several character-istic lengths calculable from a knowledge of the !-machine andconsider their implications for the long range order so ubiqui-tous in polytypes; and in §5 we give our conclusions and direc-tions for future work. In a companion paper we apply !MSRto DPs obtained from single crystal X-ray diffraction experi-ments (Varn et al., 2007).

2. Methods

We use the same notational conventions and definitions intro-duced previously (Varn et al., 2013). For each example we beginwith a stacking structure as described by an !-machine. We gen-erate a sample sequence from the !-machine of length 400 000in the Hagg notation. We map this spin sequence into a stack-ing orientation sequence in the ABC notation. We directly scanthis latter sequence to find the two-layer correlation functions(CFs): Qc(n), Qa(n) and Qs(n) (Yi & Canright, 1996). For thedisordered stacking sequences we treat here, the CFs typicallydecay to an asymptotic value of 1/3 for large n. We set theCFs to 1/3 when they reach " 1% of this value, which usu-ally occurs for n " 25 # 100. We then calculate the correcteddiffracted intensity per ML, I(") (Varn et al., 2013) in incre-ments of 6" = 0.001 using equations (1) and (2) of Varn etal. (2013) with a stacking sequence of 10 000 MLs. Through-out we refer to the corrected diffracted intensity per ML, I("),as simply the DP. We now take this simulated DP as our “exper-imental” DP.

We apply !MSR (Table 1 of Varn et al. (2013)) to each exper-imental DP. Since these are simulated DPs, we find that thefigures-of-merit, # and $, are equal to their theoretical valueswithin numerical error over all unit "-intervals. Therefore, wedo not report # and $, and instead perform !MSR over the inter-val 0 $ " $ 1. Further, again since these are simulated DPs andhence have no error, we are not able to set an acceptable thresh-old error K in advance. Instead, each example, except for Exam-ple C, minimally requires the r = 3 solutions. Thus, we solvethe spectral equations (SEs) at r = 3 (Appendix A.3 of Varnet al. (2013)) via a Monte Carlo technique (Varn, 2001) to findsequence probabilities of length-4. We take the r = 3 !-machinegiven in Fig. 2 of Varn et al. (2013) as our default or candi-date !-machine. All causal states (CSs) and allowed transitionsbetween CSs are initially assumed present. From the sequenceprobabilities we estimate the transition matrices, T(s)

Si"S j, for

making a transition from a candidate CS S i to a candidate CS S jon seeing a spin s. We apply the equivalence relation, equation(11) of Varn et al. (2013), to generate a final set of CSs. We referto the resulting !-machine as the reconstructed or “theoretical”r = 3 !-machine for the DP. In the event that the reconstructed

2 We note that there are no inherent obstacles to applying !MSR to materials with more complicated MLs or stacking rules (Brindley, 1980; Thompson, 1981; Varn& Canright, 2001). However, the case of CPSs is by no means merely academic, since several important polytypes, such as SiC and ZnS, are describable as CPSs.

2 Varn, Canright & Crutchfield · !MSR - Simulation Studies Acta Cryst. (0000). A00, 000000

!-machine assigns to a CS an asymptotic state probability of lessthan 0.01, we take that CS to be nonexistent. We use the samemethod to find the CFs and the DP for the theoretical !-machineas we did with the initial !-machine.

We also calculate the information-theoretic quantitiesdescribed in §3.1 of Varn et al. (2013) for each example andthe reconstructed !-machine.3

We find that the most calculationally intensive portion of!MSR is solving the SEs at r = 3. Even so, this is generallyaccomplished within a few minutes on desktop computer with! 2 GHz Intel Core i7 processor and several GBs of RAM. Theother steps in the reconstruction process require no more thana few seconds of computer time. It is likely that the r = 4 SEs(not treated here) can be solved in a comparable time frame.The SEs become quite cumbersome at r = 5, and it is unlikelythat they are as easily solvable with currently available desktoptechnology. However we strongly suspect that further investi-gation will reveal alternate algorithms that will eliminate somethese calculational difficulties for larger r.

3. Analysis

3.1. Example A

We begin with the sample process given in Fig. 1. One pos-sible way to interpret this !-machine is to decompose it intocausal state cycles (CSC) (Varn et al., 2013), denoted here bythe sequence of CSs enclosed in square brackets []. If one doesthis, then one might associate the following crystal and faultstructures with CSCs:4

2H [S2S5]3C+ [S7]Deformation fault [S5S3S7S6], [S2S4S0S1]Growth fault [S5S3S6], [S2S4S1]

where the “+” on 3C indicates that only the positive chirality(. . . 1111 . . .) structure is present. The faulting is given with ref-erence to the 2H crystal.5

The DP from this process is shown in Fig. 2. The experi-enced crystallographer has little difficulty guessing the under-lying crystal structure: the peaks at " " 0.50 and at " " 1.00indicate 2H structure; while the peak at " " 0.33 is characteris-tic of the 3C structure.

The faulting structure is less clear, however. It is knownthat various kinds of faults produce different effects on theBragg peaks (Sebastian & Krishna, 1994). For instance, bothgrowth and deformation faults broaden the peaks in the DP the2H structure. The difference is that growth faults broaden theinteger-" peaks three times more than the half-integer-" peaks,while peaks broadened due to deformation faulting are aboutequal. The full-width at half maximum (FWHM) for the peaks

are 0.028, 0.034, and 0.049 for " " 0.33, 0.5, and 1, respec-tively. This gives, then, a ratio of about 1.4 for the integer-" tohalf-integer-" broadening, suggesting (perhaps) that deforma-tion faulting is prominent. One expects there to be no shift in theposition of the peaks for either growth or deformation faulting;which is not the case here. In fact, the two peaks associated withthe 2H structure at " " 0.50 and 1.00 are shifted by 6" " 0.006and 0.009, respectively. This analysis is, of course, only justi-fied for one parent crystal in the overall structure, nonetheless ifwe neglect the peak shifts, the simple intuitive analysis appearsto give good qualitative results here.

With the 3C peak, both deformation and growth faults pro-duce a broadening, the difference being that the broadening isasymmetrical for the growth faults. One also expects there tobe some peak shifting for the deformation faulting. There is aslight shift (6" " 0.002) for the " " 0.33 peak and the broaden-ing seems (arguably) symmetric, so one is tempted to guess thatdeformation faulting is important here. Indeed, [S 7S6S5S3] isconsistent with deformation faulting in the 3C crystal. Heuris-tic arguments, while not justified here, seem to give qualitativeagreement with the known structure.

The !-machine description does better. The reconstructed !-machine is equivalent to the original one, with CS probabilitiesand transition probabilities typically within 0.1% of their origi-nal values, except for the transition probability from from S 4 toS1, T(1)

S4"S1= 0.33, which was 1% too small. Not surprisingly,

the process shown in Fig. 1 is the reconstructed !-machine andso we do not repeat it.

The two-layer CFs Qs(n) versus n from the process and fromthe reconstructed !-machine are shown in Fig. 3. The differ-ences are too small to be seen on the graph. We calculate theprofile R-factor (Varn et al., 2013) to compare the experimen-tal DP (Example A) to the theoretical DP (reconstructed !-machine) and find a value of R = 2%. If we generate sev-eral DPs from the same process, we find profile R-factors ofsimilar magnitude. This error then must be due to sampling.It stems from the finite spin sequence length we use to cal-culate the CFs and our method for setting them equal to theirasymptotic value. This can be improved by taking longer sam-ple sequence lengths and refining the procedure for setting theCFs to their asymptotic value. Since profile R-factors compar-ing theory and experiment are typically much larger than this,at present, this does not seem problematic. A comparison of thetwo DPs is shown in Fig. 2. This kind of agreement is typicalof !MSR from any process that can be represented as a r = 3!-machine (Varn, 2001).

We find by direct calculation from the !-machine that bothExample A and the reconstructed process have a configura-tional entropy of hµ = 0.44 bits/ML, a statistical complexityofCµ = 2.27 bits, and an excess entropy of E = 0.95 bits.

3 Although we restrict our attention to those computational quantities defined in Varn et al. (2013), there have recently been other information-theoretic measuresproposed to characterize complexity and natural information processing in materials (Cartwright & Mackay, 2012).4 A detailed survey of the structure of the !-machine containing faulting sequences is a current topic of research. An approximate scheme relating faulting structuresto causal state paths on an !-machine is given in Varn (2001).5 Here and elsewhere, we use the Ramsdell notation to specify crystalline stacking structures in CPSs. Recall that the !-machine gives stacking sequences in termsof the Hagg notation.


Example A illustrates several points. (i) For processes that arerepresentable as an r = 3 !-machine, the reconstruction proce-dure typically reproduces the !-machine within numerical error.(ii) The !-machine can accommodate two distinct crystal struc-tures (3C and 2H) and the faulting between them. (iii) Althoughthe faulting was weak enough so that the DP retained Bragg-likepeaks, we did not need to incorporate this information into thereconstruction procedure. !MSR detected the underlying crystalstructures without explicit intervention. (iv) !MSR has no dif-ficulty modeling crystals that are not spin inversion symmetric(i.e. 0 ! 1) (Varn & Canright, 2001). That is, !MSR correctlyfound that only the positive chirality 3C structure was present.

3.2. Example B

Upon annealing, solid-state transformations can occur inmany polytypes (Sebastian & Krishna, 1994). Here, we attemptto model twinned 3C structures in the presence of 6H struc-ture. However, since two crystal structures represented on an!-machine cannot share a CS, an r = 3 !-machine has an insuf-ficient memory to capture simultaneously both 3C and the 6Hstructures. For example, on an r = 3 !-machine, 3C+ and 6Hshare the stacking sequence 111 and, hence, each must visit S 7.The transition probabilities from this latter CS cannot specifyboth that the next symbol have a high probability of being 1(and thus create 3C+) and a high probability of being 0 (andthus generate 6H). In fact, it is necessary to use an r = 4 !-machine to encompass both structures.

The r = 4 !-machine in Fig. 4 does just this.[R1R3R7R14R12R8] is the CSC associated with 6H, althoughthe probability of repeating this CSC more than once is lowowing to the transition probabilities out of CSs R7 andR8. [R0]and [R15] give the twinned 3C structures.

Employing spectral reconstruction, we find the r = 3 !-machine shown in Fig. 5. All CSs are present and all transitions,save those that connect S2 and S5, are present. A comparison ofthe CFs for the original process and the reconstructed !-machineis given in Fig. 6. The agreement is remarkably good. It seemsthat the r = 3 !-machine picks up most of the structure in theoriginal process.

There is similar, though not as good, agreement in the DPs,as Fig. 7 shows. The most notable discrepancies are in the smallrises at " " 0.17 and " " 0.83. We calculate a profile R-factorof R = 12% between the diffraction spectra for Example B andthe reconstructed !-machine. The r = 3 !-machine has difficultyreproducing the 6H structure in the presence of 3C structure, asexpected.

Given the good agreement between the CFs and the DPs gen-erated by Example B and the r = 3 !-machine, we are led toask what the differences between the two are. In Table 3 wegive the frequencies of the eight length-3 sequences generatedby each process. The agreement is excellent. They both givenearly the same probabilities (! 0.32) for the most commonlength-3 sequences, 111 and 000. Example B does forbid twolength-3 sequences, 101 and 010, which the reconstructed r = 3!-machine allows with a small probability (! 0.03). At the levelof length-3 sequences, the !-machine is capturing most of the

structure in the stacking sequence.A similar analysis allows us to compare the probabilities of

the 16 length-4 sequences generated by each; the results aregiven in Table 4. There are more striking differences here. Thefrequencies of the two most common length-4 sequences inExample B, Pr(Ex)(1111) = Pr(Ex)(0000) = 0.227, are over-estimated by the r = 3 !-machine, which assigns them a prob-ability of Pr(Th)(1111) " Pr(Th)(0000) " 0.30 each. Similarly,sequences forbidden by Example B—1101, 1011, 1010, 1001,0110, 0101, 0100, 0010—are not necessarily forbidden by ther = 3 !-machine. In fact, the r = 3 !-machine forbids onlytwo of them, 0101 and 1010. This implies that r = 3 !-machinecan find spurious sequences that are not in the original stack-ing sequence. This is to be expected. But the r = 3 !-machinedoes detect important features of the original process. It findsthat this is a twinned 3C structure. It also finds that 2H struc-ture plays no role in the stacking process. (We see this by theabsence of transitions between S2 and S5 in Fig. 5.)

We can also compare the probability that each !-machineassigns to seeing a 111000 sequence, the sequence that gen-erates the 6H structure. For Example B, direct calculation fromthe !-machine, Fig. 4, gives a probability of Pr (Ex)(111000) =0.09. In contrast, a similar calculation from the theoretical !-machine, Fig. 5, gives a much lower value, Pr (Th)(111000) =0.006. This discrepancy is directly related to the fact that 3Cand 6H share the S0 and S7 CSs and, thus, the r = 3 !-machinecannot simultaneously model both 3C and 6H structure.

We find by direct calculation that the Example B processhas a configurational entropy of hµ = 0.51 bits/ML, a statis-tical complexity of Cµ = 2.86 bits, and an excess entropy ofE = 0.82 bits. The reconstructed process gives similar resultswith a configurational entropy hµ = 0.54 bits/ML, a statisti-cal complexity of Cµ = 2.44 bits, and an excess entropy ofE = 0.83 bits.

Example B illustrates several points. (i) It is possible, at leastin some cases, to model an r = 4 process on an r = 3 !-machine. It is likely, though, that !MSR at r = 3 will fail forsome processes not describable by an r = 3 !-machine. We dis-cuss this in more detail in §3.5. (ii) Even though !MSR doesnot detect the true process here, it does reveal important struc-tural features of that process. (iii) The sequence probabilitiesfound from solving the spectral equations can differ from thoseof the true process and !MSR can assign small probabilities tosequences forbidden by the true process.

3.3. Example C

We treat this next system, Example C, to contrast it with thelast and to demonstrate how pasts with equivalent futures aremerged to form CSs. The !-machine for this system is shownin Fig. 8 and is known as the Golden Mean Process. The rulefor generating the Golden Mean Process is simply stated: a 0or 1 are allowed with equal probability unless the previous spinwas a 0, in which case the next spin is a 1. Clearly then, thisprocess needs to only remember the previous spin and, hence,it has a memory length of r = 1. It forbids the sequence 00and all sequences that contain this as a subsequence. The pro-


cess is so-named because the total number of allowed sequencesgrows with sequence length at a rate given by the golden mean% = (1 +

%5)/2.

We employ the !MSR algorithm and find the !-machine given(again) in Fig. 8 at r = 1. A comparison of the CFs from Exam-ple C and the Golden Mean Process are given in Fig. 9. Thedifferences are too small to be seen. We next compare the DPs,and these are shown in Fig. 10. We find excellent agreement andcalculate a profile R-factor of R = 2%. At this point !MSRshould terminate, as we have found satisfactory agreement (towithin the numerical error of our technique) between “experi-ment”, Example C, and “theory”, the reconstructed !-machine.

Let us suppose that instead, we increment r and follow the!MSR algorithm as if the agreement at r = 1 had been unsatis-factory. In this case, we would have generated the “!-machine”shown in Fig. 11 at the end of step 3b (Table 1 of Varn etal. (2013)). We have yet to apply the equivalence relation, equa-tion (11) of Varn et al. (2013), and so let us call this the non-minimal !-machine. That is, we have not yet combined pastswith equivalent futures to form CSs, step 3c (Table 1 of Varn etal. (2013)). Let us do that now.

We observe that the state S2 is different from the other two,S1 and S3, in that one can only see the spin 1 upon leavingthis state. Therefore, it cannot possibly share the same futuresas S1 and S3, so no equivalence between them is possible.However, we do see that Pr(1|S1) = Pr(1|S3) = 1/2 andPr(0|S1) = Pr(0|S3) = 1/2 and, thus, these states share thesame probability of seeing futures of length-1. More formally,we can write

T(s)01"1s = T(s)

11"1s . (1)

Since we are labeling the states by the last two symbols seen atr = 2, within our approximation they do have the same futuresand so S1 and S3 can be merged to form a single CS. The resultis the !-machine shown in Fig. 8.

In general, in order to merge two histories, we check thateach has an equivalent future up to the memory length r. Inthis example, we need only check futures up to length-1 since,after the addition of one spin (s), each is labeled by the samepast; namely, 1s. Had we tried to merge the pasts 11 and 10,we would need to check all possible futures after the additionof two spins, after which the states would have the same futures(by assumption). That is, we would require

T(s)11"1s = T(s)

10"0s (2)

and

T(s!)1s"ss! = T(s!)

0s"ss! (3)

for all s and s#.

We find by direct calculation from the !-machine that bothExample C and the reconstructed process have a configura-tional entropy of hµ = 0.67 bits/ML, a statistical complexityofCµ = 0.92 bits, and an excess entropy of E = 0.25 bits.

Example C illustrates several important aspects of !MSR. (i)We explicitly demonstrate the merging of pasts that have equiv-alent futures. Thus, !MSR builds a model (within the space ofMarkov processes) that invokes the least complexity to describethe spectrum. (ii) With hµ = 0.67 bits/ML,6 Example C has sig-nificant disorder. Nonetheless, !MSR has no difficulty findingthe true process. (iii) !MSR needs no a priori information aboutthe underlying crystal structure. Indeed, Example C really doesnot have any underlying crystal structure. (iv) As with Exam-ple A, the fact that this process does not have spin inversionsymmetry presents no difficulties.

3.4. Example D

We now consider a simple finite-state process that cannot berepresented by a finite-order Markov process, called the EvenProcess (Crutchfield & Feldman, 2003; Crutchfield, 1992), asthe previous examples could. The Even Language (Hopcroft &Ullman, 1979; Badii & Politi, 1997) consists of sequences suchthat between any two 0s either there are no 1s or an even num-ber of 1s. In a sequence, therefore, if the immediately precedingspin was a 1, then the admissibility of the next spin requiresremembering the evenness of the number of previous consecu-tive 1s, since seeing the last 0. In the most general instance, thisrequires an indefinitely long memory and so the Even Processcannot be represented by any finite-order Markov chain.

We define the Even Process as follows: If a 0 or an evennumber of consecutive 1s were the last spin(s) seen, then thenext spin is either 1 or 0 with equal probability; otherwise thenext spin is 1. While this might seem somewhat artificial forthe stacking of simple polytypes, one cannot exclude this classof (so-called sofic) structures on physical grounds. Indeed, suchlong-range memories may be induced in solid-state phase trans-formations between two crystal structures (Kabra & Pandey,1988; Varn & Crutchfield, 2004). It is instructive, therefore,to explore the results of our procedure on processes with suchstructures.

Additionally, analyzing a sofic process provides a valuabletest of !MSR as practiced here. Specifically, we invoke a finite-order Markov approximation for the solution of the r = 3 equa-tions, and we shall determine how closely this approximates theEven Process with its effectively infinite range.

The !-machine for this process is shown in Fig. 12. Its causal-state transition structure is equivalent to that in the !-machinefor the Golden Mean Process. They differ only in the spins emit-ted upon transitions out of the S1 (Seven) CS. It seems, then, thatthis process should be easy to detect.

The result of !-machine reconstruction at r = 3 is shown inFig. 13. Again, it is interesting to see if the sequences forbidden

6 For comparison, a completely random stacking of MLs for CPSs would have hµ = 1 bit/ML.7 We do note that the solution of the SEs at r = 3 assigns the sequences 0100 and 0010 a small probability, Pr(Th)(0100) ! Pr(Th)(0010) ! 0.005, which impliesthat the sequence 010 is also present with a small probability, Pr(Th)(010) < 0.01. Since this falls below our threshold, we take this CS as being nonexistent. Forthis example, probabilities of this small magnitude are not meaningful, as the SEs at r = 3 are difficult to satisfy with purely real probabilities. We also note that thesolution of the SEs at r = 2 does forbid the 010 sequence. For additional discussion, see Varn (2001).


by the Even Process are also forbidden by the r = 3 !-machine.One finds that the sequence 010—forbidden by the process—is also forbidden by the reconstructed !-machine. This occursbecause S2 is missing.7 We do notice that the reconstructed !-machine has much more “structure” than the original process.We now examine the source of this additional structure.

Let us first contrast differences between !MSR and other !-machine reconstruction techniques, taking the subtree-mergingmethod (SMM) (Crutchfield & Young, 1989; Hansen, 1993;Crutchfield, 1994) as the alternative prototype. There are twomajor differences. First, since here we estimate sequence prob-abilities from the DPs and not a symbol sequence, we find itnecessary to invoke the memory-length reduction approxima-tion (Varn et al., 2013) at r & 3 to obtain a complete set ofequations. Specifically, we assume that (i) only histories up torange r are needed to make an optimal prediction of the nextspin and (ii) we can label CSs by their length-r history.

We can test these assumptions in the following way. For (i),we compare the frequencies of length-4 sequences obtainedfrom each method. This is shown in Table 5. The agreementis excellent. All sequence frequencies are within ±0.01 of thecorrect values. The small differences are due to the memory-length reduction approximation. So this does have an effect, butit is small here.

To test (ii), we can compare the !-machines generated fromeach method given the same “exact” or “correct” length-4sequence probabilities. Doing so, SMM gives the !-machinefor the Even Process shown in Fig. 12. !MSR gives a differentresult. After merging pasts with equivalent futures, one finds the!-machine shown in Fig. 15. For clarity, we explicitly show thelength-3 sequence histories associated with each CS, but do notwrite out the asymptotic state probabilities.

The !-machine generated by !MSR is in some respects asgood as that generated by SMM. Both reproduce the sequenceprobabilities up to length-4 from which they were estimated.The difference is that for !MSR, our insistence that historiesbe labeled by the last r-spins forces the representation to beMarkovian of range r. Here, a simpler model for the process, asmeasured by the smaller statistical complexity (Cµ = 0.92 bitsas compared to 1.92 bits), can be found. So, the notion of min-imality is violated. That is, !MSR searches only a subset of thespace from which processes can belong. Should the true pro-cess lie outside this subset (Markovian processes of range r),then !MSR returns an approximation to the true process. Theapproximation may be both more complex and less predictivethan the true process. It is interesting to note that had we givenSMM the sequence probabilities found from the solutions of theSEs, we would have found (within some error) the !-machinegiven in Fig. 12.

We find, then, that there are two separate consequences toapplying !MSR that affect the reconstructed !-machine. Thefirst is that for r & 3, the memory-length reduction approxi-mation must be invoked to obtain a complete set of equations.This approximation limits the histories treated and can affect thevalues estimated for the sequence probabilities. The second isthe state-labeling scheme. Only for Markovian (nonsofic) pro-

cesses can CSs be labeled by a unique finite history. Makingthis assumption effectively limits the class of processes one candetect to those that are block-r Markovian. To see this moreclearly, we can catalog the possible histories that lead to thetwo CSs in Fig. 12. In doing so, we find that the histories 000,011, 110, 100, and 100 always leave the process in CS S even.Similarly, the histories 001 and 101 always leave the processin CS Sodd. But having seen the history 111 does not specifythe CS as one can arrive in both CSs from this history. So thelabeling of CSs by histories of a finite length fails here.

Then, why do we not find sequence probabilities by solvingthe SEs, using SMM to reconstruct the !-machine? There aretwo reasons. The first is that in general one must know sequenceprobabilities for longer sequences than is necessary for !MSR.Solving the SEs for these longer sequence frequencies is oner-ous. The second is that error in the sequence probabilities foundfrom solving the SEs for these longer sequences makes identi-fying equivalent pasts almost impossible. The Even Process isan exception here, since one needs to consider only futures oflength-1. This is certainly not the case in general.

Having explored the differences between !MSR and SSM,we now return to a comparison between CFs and DPs gener-ated by the !MSR and the Even Process. The CFs for the EvenProcess and the reconstructed !-machine are given in Fig. 14.We see that both decay quite quickly to their asymptotic valuesof 1/3. There is good agreement, except in the region between5 ! n ! 10. Examining the DPs in Fig. 16, we see that thereis likewise good agreement except in the region 0.7 ! " ! 0.9.We calculate the profile R-factor between the theoretical andexperimental DPs to be R = 9%.

We find by direct calculation from the Even Process that ithas a configurational entropy of hµ = 0.67 bits/ML, a statis-tical complexity of Cµ = 0.92 bits, and an excess entropy ofE = 0.91 bits. The reconstructed !-machine gives information-theoretic quantities that are rather different. We find a configu-rational entropy hµ = 0.79 bits/ML, a statistical complexity ofCµ = 2.58 bits, and an excess entropy of E = 0.21 bits.

One reason that the reconstructed !-machine gives CFs andDPs in such good agreement with the Even Process in spiteof the fact that the information-theoretic quantities are differ-ent is the insensitivity of the CFs and DPs to the frequenciesof individual long sequences: equation (9) of Varn et al. (2013)sums sequence probabilities to find CFs. The fact that the EvenProcess has such a long memory is masked by this. However,information-theoretic quantities are sensitive to the structureof long sequences. !MSR at r = 4 should prove interesting,in this light, since the Even Process picks up another forbid-den sequence—01110—and this additional structure would bereflected in the reconstructed !-machine.

Example D illustrates several significant features of !MSR.(i) Most importantly, !MSR is limited to discovering Markovprocesses only. (ii) !MSR can result in an !-machine that ismore complex than the original process, (2.58 bits vs. 0.92 bits)but less predictive (0.79 bits/ML vs. 0.67 bits/ML). Nonethe-less, the resultant !-machine does approximate the true process.(iii) As in Example C, we find that !MSR is applicable for DPs


where there is large diffuse scattering and no Bragg peaks and,thus, high disorder and no discernible underlying crystal struc-ture.

3.5. Challenges when Applying !MSRWe have considered four examples that demonstrate success-

ful applications of !MSR. We have found instances, however,when !MSR has difficulties converging to a satisfactory result.We now analyze each step in !MSR as given in Table 1 of Varnet al. (2013) and discuss possible problems that may be encoun-tered. We concentrate here on issues that arise primarily in theapplication of !MSR. There are of course many experimentalconsiderations that frustrate the analysis of diffraction patternsin layered materials, some of which are discussed in, e.g., Vel-terop et al. (2000).

Step 1. Several problems can arise here due to data quality. Oneis that the figures-of-merit, $ and #, are sufficiently differentfrom their theoretical values over all possible "-intervals that!MSR should not even be attempted. Even if one does find aninterval such that they indicate satisfactory DPs, it is possiblethat the CFs extracted over this interval are unphysical. That is,there is no guarantee that all of the CFs are both positive andless than unity. In such a case, no stacking of MLs can repro-duce these CFs. Finally, if error ranges have not been reportedwith the experimental data, it may not be possible to set theerror threshold K.Step 2. The Pr(&r) solutions to the SEs are not guaranteed to beeither real or positive for r & 3. If this is so, then no physicalstacking of MLs can reproduce the CFs from the DP.Step 3. Given Pr(&r) that satisfy the elementary conditions ofprobability (i.e., there is no difficulty at step 2), step 3 will returna machine that generates Pr(& r). It is possible, however, thatthe resulting CSs are not strongly connected, and thus the resultmay not be interpreted as a single !-machine.Step 4. There are no difficulties here.Step 5. It is possible that one is required to go to an r that is cum-bersome to calculate. In this case, one terminates the procedurethrough practicality.

We find that the roots of these difficulties can be ultimatelytraced to four problems: (i) excessive error in the DP, (ii) theprocess has statistics that are too complex to be captured by afinite-range Markov process, (iii) the memory-length approxi-mation is not satisfied, and (iv) the initial assumptions of poly-typism are violated. We are likely to discover (i) in step 1. For(ii) and (iii), we find no difficulties at step 1, but rather at steps2, 3, and 5. For (iv), we have not examined this case in detail.However, we expect that if the assumptions of the stacking ofMLs (see §2.1 of Varn et al. (2013)) are not met then, since Eq.(1) of Varn et al. (2013) is no longer valid, the CFs found byFourier analysis will not reflect the actual correlations betweenMLs. This will likely be interpreted as poor figures-of-merit,and !MSR will terminate at step 1.

Of the four possible difficulties only (ii) and (iii) should beconsidered to be inherent to !MSR. It is satisfying that !MSRcan detect errors in the DP and then stop, so that it does notgenerate an invalid representation that simply describes “error”or “noise”.

4. Characteristic Lengths in CPSs

We now return to one of the mysteries of polytypism, namelythat of the long-range order which they seem to possess. It isof interest, then, to ask what, if anything, the spectrally recon-structed !-machine indicates about the range of interactionsbetween MLs. In this section, we discuss and quantify severalcharacteristic lengths that can be estimated from reconstructed!-machines.

(i) Correlation Length, 'c. From statistical mechanics, we havethe notion of a correlation length (Binney et al., 1993; Yeo-mans, 1992), which is simply the characteristic length scaleover which “structures” are found. The correlation functionsQc(n), Qa(n), and Qs(n) are known to decay exponentially to1/3 for many disordered stackings (Estevez-Rams et al., 2003). 8We therefore define the correlation length, 'c, as the charac-teristic length over which correlation information is lost withincreasing separation n. More precisely, let us define ^q(n) as

^q(n) =!

"

"""Q"(n) # 13

""" , (4)

so that ^q(n) gives a measure of the deviation of the CFs fromtheir asymptotic value. Then we say that

^q(n) ' “oscillating term” ( 2$n/#c . (5)

For those cases where the CFs do not decay to 1/3, we saythat the correlation length is infinite. We find that exponentialdecay is not always obeyed, but it seems to be common, 9 andthe correlation length thus defined gives a useful measure of therate of coherence loss as n increases. Our definition of correla-tion length is similar to the characteristic length L defined byShrestha & Pandey (1996; 1997).

(ii) Recurrence Length, P . For an exactly periodic process, theperiod gives the length over which a template pattern repeatsitself. We can generalize this for arbitrary, aperiodic processesin the following way. Let us take the recurrence length P asthe geometric mean of the distances between visits to each CSweighted by the probability to visit that CS:

P )#

Si%ST pii , (6)

where Ti is the average distance between visits to a CS and pi is8 There are some exceptions to this. See Kabra & Pandey (1988), Yi & Canright (1996), and Varn (2001) for examples.9 The exponential decay of correlations is discussed by Crutchfield & Feldman (2003).


the probability of visiting that CS. Then,

P =#

Si%S(2log2 Ti)pi

=#

Si%S2$pi log2 pi

= 2$$

Si"Spi log2 pi

= 2Cµ , (7)

where we have used the relation Ti = 1/pi.For periodic processes, Cµ = log2 P and so P is simply a

process’s period. For aperiodic processes P gives a measure ofthe average distance over which the !-machine returns to a CS.Notice that this is defined as the average recurrence length inthe Hagg notation. For cubic and rhombohedral structures, forexample, this is one-third of the physical repeat distance in theabsolute stacking sequence.(iii) Memory Length, r". Recall from §3.1 of Varn etal. (2013) that the memory length is an integer which specifiesthe maximum number of previous spins that one must know inthe worst case to make an optimal prediction of the next spin.For an rth-order Markov process this is r.(iv) Interaction Length, rI . The interaction length is an integerthat gives the maximum range over which spin-spin interactionsappear in the Hamiltonian.

We calculated the 'c, P , and r" (in units of MLs) for Exam-ples A-D as well as for three crystal structures and a completelyrandom stacking of MLs (that still obey the stacking constraintshowever). The results are displayed in Table 7. We see that eachcaptures a different aspect of the system. The correlation length'c sets a scale over which a process is coherent. For crystals,as shown in Table 7, this length is infinite. For more disorderedsystems, this value decreases. The generalized period P is ameasure of the scale over which the pattern produced by theprocess repeats. The memory length r" is most closely relatedto what we might think as the maximum range of “influence” ofa spin. That is, it is the maximum distance over which one mightneed to look to obtain information to predict a spin’s value.

For periodic, infinitely correlated systems, spins at large sep-aration carry information about each other, as seen in crystals.But this information is redundant. Outside a small neighbor-hood one gets no additional information by knowing the orien-tation a spin assumes. Notice that one can have an infinite mem-ory length with a relatively small correlation length, as seen forthe Even Process (Example D). That is, even though on averagethe knowledge one has about a spin may decay, there are stillconfigurations in which distantly separated spins carry informa-tion about each other that is not stored in the intervening spins.

If we know the !-machine for a process, then we can directlycalculate 'c, P , and r". How, then, do these relate to the interac-tion length rI? Infinite correlation lengths can be achieved withvery small rI , as in the case of simple crystals. So correlationlengths alone imply little about the range of interactions. For aperiodic system in the ground state, the configuration’s period

puts a lower bound on the interaction length via r I & log2 P ,barring fine tuning of parameters, such as found at the mul-tiphase boundaries in the ANNNI model (Yeomans, 1988) orthose imposed by symmetry considerations (Canright & Wat-son, 1996; Yi & Canright, 1996; Varn & Canright, 2001). Themost likely candidate for a useful relation between r I and aquantity generated from the !-machine is r ". Indeed, r" sets alower bound on rI , if the system is in equilibrium. For poly-types, the multitude of observed structures suggests that mostare not in equilibrium but rather trapped in nonequilibriummetastable states. Consequently, one does not know what therelation between rI and r" is. It is conceivable, especially in themidst of a solid-state phase transition, that small rI could gener-ate large r" (Varn & Crutchfield, 2004). While an !-machine isa complete description of the underlying stacking process, onemust additionally require that the material is in equilibrium inorder to make inferences concerning r I . This reflects the differ-ent ways in which a Hamiltonian and an !-machine describe amaterial.

5. Conclusions

We demonstrated the feasibility and accuracy of !-machinespectral reconstruction by applying it to four simulated DPs.In each case, we find that !MSR either reproduces the statisticsof the stacking structure, as for Examples A and C, or finds aclose approximation to it. Elsewhere, we applied the same pro-cedures to the analysis of experimental DPs from single-crystalplanar faulted ZnS, focusing on the novel physical and mate-rial properties that can be discovered with this technique (Varnet al., 2007).

It is worthwhile to return one final time to some of the impor-tant features of !MSR. (i) !MSR makes no assumptions abouteither the crystal or faulting structures that may be present.Instead, using correlation information as input, !MSR con-structs a model of the stacking structure—in the form of an!-machine—that reproduces the observed correlations. There-fore, the algorithm need not rely on the experience or ingenu-ity of the researcher to make a priori postulates about crystalor fault structure. (ii) As the analysis of Example A shows,!MSR is able to detect and describe stacking structures thatcontain multiple crystal and fault structures. Indeed, ExampleA represented a crystal that was predominately 2H, but also hadsignificant portions of 3C crystal structure. Additionally, twofaulting structures, growth and deformation faults, were iden-tified. (iii) Since !MSR does not need to assume any under-lying crystal structure, it can detect and describe even highlydisordered structures. Example C has significant disorder (hµ

= 0.67 bits/ML) and does not contain any readily identifiablecrystal structure. Nevertheless, !MSR is capable of finding anddescribing the statistics of even such highly disordered stack-ing structures. (iv) !MSR uses all of the information availablein a DP. By integrating the DP over a unit interval in recipro-cal space to find the CFs, !MSR makes no distinction betweendiffuse scattering and Bragg-like peaks. Each is treated equally.Indeed, even though Example B shows both Bragg-like peaksas well as considerable diffuse scattering between peaks, !MSR


naturally captures the information contained in both by inte-grating over the entire DP. (v) It is advantageous not to invokea more complicated explanation than is necessary to understandexperimental data. By initially assuming a small memory lengthand incrementing this as needed to improve agreement betweentheory and experiment, as well as merging stacking “histories”with equivalent “futures”, !MSR builds the smallest possiblemodel that reproduces the experimentally observed DP withoutover-fitting the data. Example C shows how !MSR is able to findthis minimal expression for the stacking structure. (vi) Finally,the resulting expression of the stacking structure, the process’s!-machine, allows for the calculation of parameters of physicalinterest. For each example, we were able to find the configu-rational entropy associated with the stacking process and thestatistical complexity of the stacking structure. In a companionpaper (Varn et al., 2007), we show how the average stackingenergy and hexagonality may be calculated from the !-machine.

Additionally, we have identified three length parameters thatare calculable from the !-machine: the correlation length, ' c;the recurrence length, P ; and the memory length, r ". Each mea-sures a different length scale over which structural organizationappears. New to this work is P , which is a generalization ofthe period of a periodic process. P is a measure of the aver-age length between visits to each CS. As such it quantifies theaverage distance over which the pattern repeats itself. Thus bothperiodic and aperiodic patterns have a characteristic length scaleafter which they begin to repeat. The last length parameter weidentified is r", the distance over which a ML can carry nonre-dundant information about the orientation of another ML. Thisis most closely related to the rI . If the assumption of equilib-rium can be made for polytypes, r" places a lower bound on rI .But the assumption of equilibrium is critical, and not likely metby many polytypes.

Even with these advantages, however, !MSR as practicedhere is not without its shortcomings. Perhaps most restrictive isthat !MSR is limited to Markov processes and has only beenworked out for 3rd-order Markov processes. Since the maxi-mum number of terms in the SEs grows as the exponential ofan exponential in the memory length, the task of writing outthe higher order SEs quickly becomes prohibitively difficult.While the r = 4 case is almost certainly tractable, the r = 5 isquestionable and r & 6 is probably not (with current methods).Although r = 3 !-machines identify much of the structure inhigher-order processes, we found two difficulties. (i) Approxi-mations made in the derivation of the SEs can result in sequenceprobabilities that differ from those of the true process, as seen inExample B. (ii) The state labeling scheme imposes a CS archi-tecture on the reconstructed !-machine that may be too restric-tive. The !-machine in Example D belonged to a class of pro-cesses, formally known as sofic processes, that have a specialkind of infinite-range memory. The CSs on the !-machines thatdescribe these processes cannot be specified by any finite his-tory. So, the scheme of labeling states by the last r-spins seen,as is done here, represents a serious drawback to !MSR.

Lastly, we note the !MSR can help give a detailed accountof how a crystal becomes disordered. In order to determine

the mechanism of faulting in, say, an annealed crystal under-going a solid-state phase transition, it is desirable to beginwith many (identical) crystals and arrest the solid-state trans-formation at various stages. By reconstructing the !-machineafter different annealing times, the route to disorder can bemade plain. The result is a picture of how structure (as cap-tured by intermediate !-machines) changes during annealing.This change in structure should give direct insight into thestructure-forming mechanisms. This should be compared withthe numerical simulation of faulting in a crystal (Kabra &Pandey, 1988; Engel, 1990; Shrestha & Pandey, 1996; Shrestha& Pandey, 1997; Gosk, 2000; Gosk, 2001; Gosk, 2003; Varn& Crutchfield, 2004). We note that in such simulations, the !-machine can be directly calculated from the sequence to highaccuracy. Some experimental work on solid-state phase transi-tions has been done (Sebastian & Krishna, 1994; Boulle et al.,2010; Dompoint et al., 2012), but we hope that this improvedtheoretical framework will stimulate additional efforts in thisdirection.

AcknowledgmentsWe thank L. J. Biven, D. P. Feldman, and E. Smith for help-

ful conversations; and P. M. Riechers and three anonymous ref-erees for comments that improved the manuscript. This workwas supported at the Santa Fe Institute under the NetworksDynamics Program funded by the Intel Corporation and underthe Computation, Dynamics and Inference Program via SFI’score grants from the National Science and MacArthur Foun-dations. Direct support was provided by NSF grants DMR-9820816 and PHY-9910217, DARPA Agreement F30602-00-2-0583, and ARO grant W911NF-12-1-0234. DPV’s visit to SFIwas partially supported by the NSF.

ReferencesBadii, R. & Politi, A. (1997). Complexity: Hierarchical Structures and

Scaling and Physics, vol. 6 of Cambridge Nonlinear ScienceSeries. Cambridge University Press.

Bataronov, I. L., Posmet’yev, V. V. & Barmin, Y. V. (2004). Ferro-electrics, 307, 191 – 197.

Binney, J. J., Dowrick, N. J., Fisher, A. J. & Newman, M. E. J. (1993).The Theory of Critical Phenomena. Clarendon Press.

Boulle, A., Dompoint, D., Galben-Sandulache, I. & Chaussende, D.(2010). J. Appl. Crystallogr. 43(4), 867–875.

Brindley, G. W. (1980). In Crystal Structures of Clay Minerals andtheir X-ray Identification, edited by G. W. Brindley & G. Brown,chap. II. London: Mineralogical Society.

Canright, G. S. & Watson, G. (1996). J. Stat. Phys. 84, 1095–1131.Cartwright, J. H. E. & Mackay, A. L. (2012). Phil. Trans. R. Soc. A,

370(1969), 2807–2822.Cheng, C., Heine, V. & Jones, I. L. (1990). J. Phys.: Condens. Matter,

2, 5097–5113.Cheng, C., Needs, R. J. & Heine, V. (1988). J. Phys. C: Solid State

Phys. 21, 1049–1063.Cheng, C., Needs, R. J., Heine, V. & Churcher, N. (1987). Europhys.

Lett. 3, 475–479.Crutchfield, J. P. (1992). In Santa Fe Studies in the Sciences of Com-

plexity, edited by M. Casdagli & S. Eubanks, vol. XII, pp. 317–359. Reading, Massachusetts: Addison-Wesley.

Crutchfield, J. P. (1994). Physica D, 75, 11–54.Crutchfield, J. P. & Feldman, D. P. (2003). Chaos, 13, 25–54.Crutchfield, J. P. & Young, K. (1989). Phys. Rev. Lett. 63, 105–108.


Dompoint, D., Boulle, A., Galben-Sandulache, I. & Chaussende, D.(2012). Nuclear Instruments and Methods in Physics ResearchSection B: Beam Interactions with Materials and Atoms, 284,19–22.

Engel, G. E. (1990). J. Phys. Cond. Mat. 2, 6905–6919.Engel, G. E. & Needs, R. J. (1990). J. Phys. Cond. Mat. 2, 367–376.Erenburg, A., Gartstein, E. & Landau, M. (2005). J. Phys. Chem.

Solids. 66, 81–90.Estevez-Rams, E., Aragon-Fernandez, B., Fuess, H. & Penton-

Madrigal, A. (2003). Phys. Rev. B, 68, 064111.Ferraris, G., Makovicky, E. & Merlino, S. (2008). Crystallography of

modular materials, vol. 15. Oxford University Press, USA.Gosk, J. B. (2000). Crys. Res. Tech. 35, 101–116.Gosk, J. B. (2001). Crys. Res. Tech. 36, 197–213.Gosk, J. B. (2003). Crys. Res. Tech. 38, 160–173.Hansen, J. E. (1993). Computational Mechanics of Cellular Automata.

Ph.D. thesis, University of California, Berkeley.Hopcroft, J. E. & Ullman, J. D. (1979). Introduction to Automata The-

ory, Languages, and Computation. Addison-Wesley.Jagodzinski, H. (1949). Acta Crystallogr. 2, 201–207.Kabra, V. K. & Pandey, D. (1988). Phys. Rev. Lett. 61, 1493–1496.Mardix, S. (1986). Phys. Rev. B, 33, 8677–8684.Melinon, P., Masenelli, B., Tournus, F. & Perez, A. (2007). Nat. Mater.

6, 479–490.Nasir, N., Shah, C., Leech, P., Reeves, G., Pirogova, E., Istivan, T.,

Tanner, P. & Holland, A. (2012). In Biomedical Engineering(ICoBE), 2012 International Conference on, pp. 589 –593.

Pandey, D. & Krishna, P. (1982). In Current Topics in Materials Sci-ence, edited by E. Kaldis. North-Holland.

Price, G. D. (1983). Phys. Chem. Minerals, 10, 77–83.Sebastian, M. T. & Krishna, P. (1994). Random, Non-Random and

Periodic Faulting in Crystals. Gordon and Breach.Shalizi, C. R. & Crutchfield, J. P. (2001). J. Stat. Phys. 104, 817–881.Shaw, J. J. A. & Heine, V. (1990). J. Phys. Cond. Mat. 2, 4351–4361.Shrestha, S. P. & Pandey, D. (1996). Europhys. Lett. 34(4), 269–274.Shrestha, S. P. & Pandey, D. (1997). Proc. R. Soc. London Ser. A, 453,

1311–1330.Thompson, J. B. (1981). In Structure and Bonding in Crystals II, edited

by M. O’Keeffe & A. Navrotsky, chap. 22. New York: AcademicPress.

Trigunayat, G. C. (1991). Solid State Ionics, 48, 3–70.Varn, D. P. (2001). Language Extraction from ZnS. Ph.D. thesis, Uni-

versity of Tennessee, Knoxville.Varn, D. P. & Canright, G. S. (2001). Acta Crystallogr. Sec. A, 57,

4–19.Varn, D. P., Canright, G. S. & Crutchfield, J. P. (2002). Phys. Rev. B.

66, 174110.Varn, D. P., Canright, G. S. & Crutchfield, J. P. (2007). Acta Crystal-

logr. Sec. B, 63, 169–182.Varn, D. P., Canright, G. S. & Crutchfield, J. P. (2013). Acta Crystal-

logr. Sec. A, 69, 197–206.Varn, D. P. & Crutchfield, J. P. (2004). Phys. Lett. A, 324(4), 299–307.Velterop, L., Delhez, R., de Keijser, T. H., Mittemeijer, E. J. & Reef-

man, D. (2000). J. Appl. Crystallogr. 33, 296–306.Wang, Z., Wang, S., Zhang, C. & Li, J. (2011). J. Nanoparticle Res.

13, 185–191.Yeomans, J. (1988). Solid State Physics, 41, 151–200.Yeomans, J. (1992). Statistical Mechanics of Phase Transitions.

Clarendon Press.Yi, J. & Canright, G. S. (1996). Phys. Rev. B, 53(9), 5198–5210.Table 1

A table for translating base ten notation into binary notation of length three.This is useful for converting the base ten subscripts of the CSs in Figs. 1, 5 and13 into the corresponding binary spin sequences.Base Base Base Base Base Base Base BaseTen Two Ten Two Ten Two Ten Two

0 000 2 010 4 100 6 1101 001 3 011 5 101 7 111

Table 2A table for translating base ten notation into binary notation of length four.This is useful for converting the base ten subscripts of the CSs in Fig. 4 into thecorresponding binary spin sequences.Base Base Base Base Base Base Base BaseTen Two Ten Two Ten Two Ten Two

0 0000 4 0100 8 1000 12 11001 0001 5 0101 9 1001 13 11012 0010 6 0110 10 1010 14 11103 0011 7 0111 11 1011 15 1111

Table 3The frequencies of length-3 sequences obtained from Example B and the !-machine reconstructed at r = 3.Sequence Example B !MSR Sequence Example B !MSR

111 0.318 0.324 011 0.091 0.070110 0.091 0.081 010 0.000 0.026101 0.000 0.027 001 0.091 0.076100 0.091 0.076 000 0.318 0.322

Table 4The frequencies of length-4 sequences obtained from Example B and the !-machine reconstructed at r = 3.Sequence Example B !MSR Sequence Example B !MSR

1111 0.227 0.300 0111 0.091 0.0251110 0.091 0.024 0110 0.000 0.0451101 0.000 0.029 0101 0.000 0.0001100 0.091 0.052 0100 0.000 0.0261011 0.000 0.027 0011 0.091 0.0461010 0.000 0.000 0010 0.000 0.0301001 0.000 0.049 0001 0.091 0.0261000 0.091 0.027 0000 0.227 0.296

Table 5The frequencies of length-4 sequences obtained from !MSR and SMM for theEven Process, Example D. At most, they differ by ±0.01.Sequence !MSR SMM Sequence !MSR SMM

1111 0.24 0.25 0111 0.09 0.081110 0.09 0.08 0110 0.07 0.081101 0.09 0.08 0101 0.00 0.001100 0.08 0.08 0100 < 0.01 0.001011 0.08 0.08 0011 0.08 0.081010 0.00 0.00 0010 < 0.01 0.001001 0.04 0.04 0001 0.05 0.041000 0.04 0.04 0000 0.04 0.04


Table 6Measures of intrinsic computation calculated from the processes of ExamplesA, B, C, and D and their (r = 3) reconstructed !-machines. For Examples A,B, and C the reconstructed !-machines give good agreement. For Example D,however, the reconstructed !-machine requires more memory and still has anentropy density hµ significantly higher than that of the Even Process. The lastcolumn gives 6 = Cµ "E" rhµ as a consistency check derived from Eq. (23)of Varn et al. (2013), which describes order-r Markov processes. Recall thatthe Even Process of Example D is not a finite-r process and so Eq. (23) Varnet al. (2013) does not hold. All one can say is that E # Cµ (Shalizi & Crutch-field, 2001), which is the case for Example D.System Range hµ [bits/ML] Cµ [bits] E [bits] 6

Example A 3 0.44 2.27 0.95 0.00!-machine 3 0.44 2.27 0.95 0.00

Example B 4 0.51 2.86 0.82 0.00!-machine 3 0.54 2.44 0.83 -0.01

Example C 1 0.67 0.92 0.25 0.00!-machine 1 0.67 0.92 0.25 0.00

Example D $ 0.67 0.92 0.91 —!-machine 3 0.79 2.58 0.21 0.00

Table 7The three characteristic lengths that one can calculate from knowledge of the!-machine: the correlation length #c, the recurrence length P , and the memorylength r". For comparison, we also give these quantities for several commoncrystalline structures as well as a completely random process.System #c P r"

Example A, r = 3 % 7.4 4.8 3Example B, r = 4 % 7.8 7.3 4Example C, Golden Mean % 4.5 1.9 1Example D, Even Process % 1.7 1.9 $3C $ 1 02H $ 2 16H $ 6 3Completely Random 1 1 0

1 | 1.00

S6(0.03)

1 | 0

.92

0 | 0.08

S7(0.26)

0 | 0.90

1 | 0.10

S5

0 | 0

.33

1 | 0.67

S3

0 | 0.67

1 | 0

.33

S4

S0

1 | 1.000 | 1.00S1

1 | 0.90

0 | 0.10

S2(0.30)

(0.03)

(0.30)

(0.03)

(0.02)

(0.03)

Figure 1The r = 3 theoretical and experimental !-machine for the Example A process.The nodes represent CSs and the directed arcs are transitions between them. Theedge labels s|p indicate that a transition occurs between the two CSs on sym-bol s with probability p. The asymptotic probabilities for each CS are given inparentheses. We label the states with the last three spins observed in base tennotation. (A chart for converting base ten into base two in given in Table 1.) Thelarge probabilities to repeat the CSCs [S7] and [S2S5] suggest that one think ofthese cycles as crystal structure and everything else as faulting.

Figure 2A comparison between the DPs I(") generated by Example A (blue solid line)and by the r = 3 spectrally reconstructed !-machine (red dashed line). The dif-ferences between the DP for Example A and the r = 3 reconstructed !-machineare too small to be seen. We calculate R = 2%, but this is largely due to numer-ical error. (See text.) The peak at " ! 1/3 corresponds to the 3C structure andthe two peaks at " ! 1/2 and " ! 1 to the 2H structure.

Figure 3A comparison of the CFs Qs(n) between the Example A process (blue dia-monds) and the r = 3 reconstructed !-machine (red squares). As with the DPsthe differences are too small to be seen on the graph. As an aid to the eye, hereand in other graphs showing CFs, we connect the the values of adjacent CFswith straight lines. The CFs, of course, are defined only for integer values of n.


0 | 1.00R14(0.09)

1 | 0

.80

0 | 0.20

R15

R12

0 | 0

.50

1 | 0.50

R7

0 | 0.50

1 | 0

.50

R8

0 | 0.80

R0

1 | 0.20

1 | 1.00R1R3

0 | 1.00

1 | 1.00

(0.09) (0.09)

(0.23)

(0.09)(0.09)(0.09)

(0.23)

Figure 4The experimental !-machine for Example B. Since it has a memory of r" = 4,we label the states with the last four spins observed: i.e., R12 means that 1100were the last four spins. (A chart for converting base ten into base two in givenin Table 2.) The CSCs [R15] and [R0] give rise to 3C structure and the CSC[R1R3R7R14R12R8] generates 6H structure.

0 | 0.61

1 | 0.39

S6(0.08)

1 | 0

.92

0 | 0.08

S7

1 | 1.00

S5

0 | 0

.64

1 | 0.36

S3

0 | 0.36

1 | 0

.64

S4

0 | 0.92

S0

1 | 0.08

1 | 0.61

0 | 0.39

S1

0 | 1.00

S2(0.03)(0.32)

(0.07)

(0.03)

(0.08)

(0.32)

(0.08)

Figure 5The reconstructed (theoretical) !-machine at r = 3 for Example B. The absenceof arcs connecting the S2 and S5 CSs indicate that !MSR has correctly identi-fied that there is no 2H structure in this crystal.

Figure 6A comparison of the CFsQs(n) generated by the r = 3 reconstructed !-machine(red squares) and generated by Example B (blue diamonds). The agreement isgenerally quite good, except for perhaps n = 3, 6, 7.

Figure 7A comparison of the DPs I(") between r = 3 reconstructed !-machine (reddashed line) and the process of Example B (solid blue line). The agreementis surprisingly good; we calculate a profile R-factor of R = 12%. The smallenhanced scattering at " ! 1/6 and " ! 5/6 corresponds to the 6H structure.The r = 3 !-machine has difficulty in reproducing these because the 6H andthe 3C structure both share the S7 and S0 CSs and so require an !-machinereconstructed at r = 4 to properly disambiguate them.

1 | 1

/2

0 | 1/2

S1

1 | 1

S0(2/3) (1/3)

Figure 8The recurrent portion of the !-machine for the Golden Mean Process, ExampleC. The process has a memory length of r = 1, and so we label each CS by thelast spin seen.

Figure 9A comparison of the CFsQs(n) generated by the r = 1 reconstructed !-machine(red squares) and the Golden Mean Process of Example C (blue diamonds). TheCFs decay quickly to their asymptotic value of 1/3.


Figure 10A comparison of the DPs for Example C (solid blue line) and the reconstructedr = 1 !-machine (dashed red line). The agreement is excellent. One finds aprofile R-factor of 2% between the experimental DP, Example C, and the the-oretical DP calculated from the reconstructed !-machine.

1 | 0.50

0 | 0.50S1

1 | 1.00

S2(0.33) (0.33)

S3(0.34)

1 | 0.50 0 | 0.50

Figure 11The r = 2 reconstructed nonminimal !-machine for the Golden Mean Pro-

cess, Example C. Applying the equivalence relation, equation (11) of Varn etal. (2013), we find that S1 and S3 have the same futures, and thus should becollapsed into a single CS. Doing so gives the !-machine in Fig. 8.

0| 0

.50

1 | 0.50

Seven

1 | 1.00

Sodd(0.67) (0.33)

Figure 12The recurrent portion of the !-machine for the Even Process, Example D. Sincethe CSs cannot be specified by a finite history of previous spins, we have labeledthem Seven and Sodd. We find that this !-machine has a statistical complexity ofCµ = 0.92 bits.

0 | 0.50

1 | 0.50

S6(0.16)

1 | 0

.73

0 | 0.27

S7

1 | 1.00

S5

0 | 0

.45

1 | 0.55S3

0 | 0.50

1 | 0

.50

S40 | 0.44

S0

1 | 0.56

1 | 1.00

S1

(0.33) (0.08)

(0.16)

(0.09)

(0.08)

(0.09)

Figure 13The r = 3 reconstructed !-machine for the Even Process of Example D.Since the Even Process forbids the sequences {012k+10, k = 0, 1, 2, . . .} andall sequences containing them, it is satisfying to see that 010 is forbidden bythe reconstructed !-machine, as evidenced by the missing S2 CS. We find thatCµ = 2.58 bits.

Figure 14A comparison of the CFsQs(n) generated by the r = 3 reconstructed !-machineand the Even Process of Example D. The CFs decay quickly to their asymptoticvalue of 1/3.


1 | 0.50

S{110,100,000}

1 | 0

.83

0 | 0.17

S{111}

1 | 1.00

S{101,001}0

| 0.5

0

1 | 0.50

S{011}

Figure 15The !-machine inferred from the exact sequence frequencies for the Even Pro-cess of Example D. The CSs are labeled with the (possibly several) length-threehistories that can lead to them. We find that Cµ = 1.92 bits.

Figure 16A comparison between the DPs I(") generated by the r = 3 reconstructed!-machine and by the Even Process of Example D. The agreement is good(R = 9%) except in the region 0.7 ! " ! 0.9. Notably, the DP for the EvenProcess has an isolated zero at " = 5/6.


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