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Mesomorphic side chain polysiloxanes : a structural study of the smectic B phase
P. Davidson, A.M. Levelut
To cite this version:
P. Davidson, A.M. Levelut. Mesomorphic side chain polysiloxanes : a structural study of the smectic B phase. Journal de Physique, 1989, 50 (17), pp.2415-2430. �10.1051/jphys:0198900500170241500�.
�jpa-00211070�
Mesomorphic side chain polysiloxanes : a structural study of
the smectic B phase
P. Davidson and A. M. Levelut
Laboratoire de Physique des Solides, associé au C.N.R.S., Université Paris XI, Bât. 510, 91405 Orsay Cedex, France
(Reçu le 30 mars 1989, accepté sous forme définitive le 25 mai 1989)
Résumé.
2014Cet article décrit une étude structurale par diffraction des rayons X de quelques polysiloxanes mésomorphes en peigne, en phase smectique B (SB ). Comme nous ne disposions
pas de véritables monocristaux, cette étude a été faite sur des échantillons alignés sous champ magnétique et présentant donc une géométrie de
«fibre
».Nous présentons d’abord la structure de cette phase SB polymère. Son organisation est similaire à celle des phases SB classiques (de mésogènes conventionnels) : les c0153urs mésogènes sont perpendiculaires aux couches et, dans une seule couche, sont empilés en un réseau hexagonal à deux dimensions. Les squelettes polymères
sont confinés entre les couches de c0153urs mésogènes, dans une épaisseur de 6 ± 1 Å le long du
directeur. Nous comparons cette structure avec celles des cristaux formés par certains polymères
de la même série et avec celles des phases SB classiques. Du premier point de vue, il semble que la
phase SB polymère puisse être considérée comme un « paracrystal » bidimensionnel ; du second, le fait que nous ne disposions pas d’un vrai monodomaine de phase SB polymère nous empêche de
l’identifier comme une phase hexatique B. Nous présentons ensuite les fluctuations qui affectent
la structure de cette phase SB polymère. Comme dans les phases SB classiques, les c0153urs mésogènes, au sein d’une couche, se placent localement aux n0153uds d’un réseau de type chevrons
avec une longueur de cohérence de l’ordre de 20 Å. De plus, dans la phase SB polymère, les squelettes corrèlent cet ordre à courte distance sur quelques couches voisines. Par ailleurs, la.
nature polymérique du composé induit une modulation transverse probablement displacive des
couches (ondulations). Sa longueur de cohérence vaut aussi environ 20 Å. Cette modulation est fortement couplée au réseau hexagonal bidimensionnel et pourrait être aussi couplée aux
fluctuations de type chevrons. Des mouvements longitudinaux des c0153urs mésogènes autour de
leurs positions moyennes dans les couches ont aussi été détectées. Certains de ces mouvements ont fréquemment été observées dans les phases SB classiques tandis que d’autres sont plus compliqués et difficiles à visualiser dans l’espace direct. Nous les analysons brièvement en termes d’ondes de déplacement transverses semblables à des phonons.
Abstract. 2014 This paper presents an X-ray diffraction study of the smectic B (SB) phase that some mesomorphic side chain polysiloxanes display. Since no true monocrystals were available, this study was performed on magnetically aligned samples which possess a fiber geometry. We have first investigated the structure of this polymeric SB phase. Its organization is similar to those of the classical SB phases (of small mesogens) : the mesogenic cores are perpendicular to the layers and, within a layer, packed on a 2D hexagonal lattice. The polymeric backbones are confined between the layers of mesogenic cores, in a width of 6 ± 1 Å along the director. We discuss this structure in Classification
Physics Abstracts
61.30 - 61.40K
Article published online by EDP Sciences and available at http://dx.doi.org/10.1051/jphys:0198900500170241500
relation to those of the crystals that some polymers of the same series display and then to those of
the classical SB phases : from the first point of view, it appears that the polymeric SB phase may be regarded as a 2 dimensional « paracrystal
».From the second one, the lack of a true monocrystal of the polymeric SB phase prevents us from definitely identifying it as a stacked
hexatic phase. We have then investigated the fluctuations which affect the structure of this
polymeric SB phase. As in classical SB phases, the mesogenic cores within a layer, pack themselves locally on a 2-dimensional herring bone array of cohérence length of the order of 20 Å. Moreover,
in the polymeric SB phase, this short range order is also correlated along a few adjacent layers by
the polymeric backbones. In addition, the polymeric nature of the compound induces a transverse probably displacive local modulation of the layers (undulations). Its cohérence length is also roughly 20 Å. This modulation is strongly coupled to the 2-dimensional hexagonal lattice and
might also be coupled to the herring bone array. Longitudinal motions of the mesogenic cores
about their mean positions in the layers have been detected too. Some of these motions are
usually seen in the classical SB phases whereas the others are more complicated and difficult to
represent in direct space. We briefly analyse them in terms of transverse displacive waves similar
to phonons.
Introduction.
Mesomorphic side chain polymers have recently attracted wide interest in view of potential applications in the field of non linear optics [1, 2]. These compounds often exhibit nematic
(N), smectic A (SA) and smectic C (Sc) phases which have been thoroughly studied.
Moreover, the smectic B (SB) phase has sometimes been reported, too [3, 4]. This paper presents a structural study of this new polymeric SB phase.
First let us recall the structure of the conventional SB phase (Hereafter, by conventional
SB phase, we mean the SB phase displayed by the usual low molecular weight liquid crystals) [5, 6] (Fig. 1) : as any smectic phase, it is characterized by the existence of layers. The mesogenic cores are perpendicular to the layers and are located within a layer on a 2D hexagonal lattice. They rotate rapidly about their long axes as was demonstrated by nuclear magnetic resonance [7] and incoherent quasielastic neutron scattering experiments [8]. In a previous paper [9], on the basis of X-ray diffraction patterns, we have detected an additional short range order : within a layer, the mesogenic cores pack themselves on a local 2D herring-
bone array. This short range order is related to the cooperative nature of the rotation of the
mesogenic cores about their long axes as was demonstrated by coherent inelastic neutron scattering experiments [10]. At long distance, the herring bone correlations vanish so that the lattice retains its hexagonal symmetry.
The conventional SB phases may be classified into two groups according to the interlayer
correlations [6, 11-13] :
-
if these correlations extend on a long range, then the molecules are 3-dimensionally
correlated and the phase is called crystal B ;
-
another phase made of stacks of 2D hexagonal lattices and called a stacked hexatic B
phase has also been predicted [11] and was observed experimentally [13]. In such a phase, one
defines the nearest neighbour bond orientational order of the hexagonal lattice. The
positional order within a layer is only short range whereas the bond orientational order remains long range and is 3-dimensionally correlated.
Let us also recall a few facts about the crystallization of polymers [14, 15]. Compared to
usual crystals (i.e. crystals of small molecules), good quality crystals of most polymers are
difficult to obtain and they contain a variable amount of amorphous material depending upon
the crystallization conditions. Their X-ray diffraction patterns display reflections which are
Fig. 1.
-Molecular organization in a layer of a conventional SB phase [6]. M : mesogenic core, C : aliphatic chain. a and b are the vectors of the hexagonal lattice. The cylinders represent the envelope of
the rotating molecules. In a crystal B phase, such layers are long range correlated along their normal and their packing eventually present superstructures. A stacked hexatic B phase is made of stacks of such
layers.
often not resolution limited and the widths of the reflections may increase with increasing scattering angle. Moreover, the intensity of these reflections usually decreases quickly with increasing scattering angle (quicker than the general decrease of the atomic form factors).
Several ideas based on the notion of disorder, account for such a behavior :
Disorders may be classified into two types [14-16] according to the statistical distributions which describe them. We shall illustrate the difference between the two types of disorder by considering their effects on the lattice vectors. If the fluctuations of two neighbouring lattice
vectors (i.e. the vectors between neighbouring lattice points) are correlated, then the disorder is called of the first type. This kind of disorder, a good example of which is thermal agitation,
does not affect the lattice long range order. Its only effect is to decrease the intensity of the
reflections by a factor of the Debye Waller type, without altering their widths which simply depend upon the size of the crystallites. If two neighbouring lattice vectors are allowed to
fluctuate independantly, then the lattice long range order is destroyed. Consequently, the
widths of the reflections do not depend only on the size of the crystallites any more but also on
the average square value of the fluctuations. Moreover, the widths of the reflections increase with the indices of the reflections, that is with increasing scattering angle ; however, their
integrated intensities are not affected. Hosemann has called « paracrystal » [14] a crystal
modified by a disorder of the second type and this concept is often used in the field of
polymeric crystals.
In this context, we found it interesting first to determine the crystallographic parameters of this new polymeric SB phase and then to study in which way the polymeric nature of the compound modifies the organization of the phase. In particular, we have tried to examine two
questions.
-
Do the ideas mentioned above, about the structures of conventional SB phases and of polymeric crystals, apply to this new polymeric SB phase ?
-
How is the local order of the mesogenic cores affected by chemically grafting them on a polymer ?
R. Duran et al. have presented an X-ray diffraction study [17] of a polymeric SE phase. They have shown that the SE phase is lamellar with the mesogenic cores packed on a
2D rectangular lattice within a layer. No 3D correlations were to be seen. These authors
consider that the polymeric SE phase may be of a hexatic nature comparable in some way to the SI phase of conventional mesogens and that the backbones are aligned along the (11) directions of the rectangular lattice, therefore strongly coupled to this lattice. The lack of well enough oriented samples did not allow the study of the mesogenic cores local order.
Among the polymers which were reported to present a SB phase in the literature, we have
chosen a series of mesomorphic side chain polysiloxanes synthesized by M. Mauzac et al. [18].
This series was already well characterized [18] and furthermore we thought that the presence of Si atoms in the backbones would increase the form factor of the molecule and give
additional information about the backbones. These polymers correspond to the formula :
and we shall call them Pn, m according to the number of methylene groups in the spacer and in the alcoxy end chain. The tacticity of these polymers has been characterized by 29Si NMR ; they can be considered as completely atactic [19].
We have chosen to study five of these polymers which were also studied by X-ray
diffraction in the SA phase [20]. Their polymorphism is recalled in table 1 :
Table I.
-Phase transition temperatures (’C) of polymers P3,4, P4,4, P3,s, P4,s and P5,8- (Tg : glass transition, Tm : melting point, Tc: clearing point) [18].
It seems that the existence of the SB phase is related to the presence of the long aliphatic
end chains [18]. Polymers P3, 4 and P4, 4 have been added so that we shall be able to compare
the polymeric SB phase with the polymeric crystals of similar compounds.
1. Experimental.
Aligned samples could be obtained by slowly cooling them (5°C/hour) from the isotropic phase to the SA phase in a magnetic field (1.7 T). These samples were contained in
Lindemann capillary tubes of 1.5 mm diameter. Therefore our samples present a cylindrical
symmetry around the magnetic field direction. In addition, a small mosaicity of about 5° exists
in our magnetically aligned samples. These magnetically aligned samples do not show as much
information as real monodomains of SB phase. Such monodomains have sometimes been obtained by melting of single crystals of low molecular weight liquid crystals [9]. However in
the present case, single crystals are unlikely to be grown due to the polymeric nature of the
compound.
The samples were examined with two different X-ray set ups :
-
a conventional Guinier camera equipped with a cylindrical quartz monochromator
(03BB CuKa 1 = 1.5405 A) helped us to measure the crystallographic parameters of the SB phase and to examine the profiles of the reflections ;
-
another set up already described [21] revealed the presence of some diffuse scattering :
a punctually focussed monochromatic X-ray beam (03BB CuKa
=1.541 À) was obtained by
reflection on a doubly bent graphite monochromator. The sample in its capillary tube is set in
an oven heated by an air stream (temperature regulation ± 1 °C). The oven is placed between
the two poles of an electromagnet. The camera is evacuated in order to suppress air-
scattering. The diffracted X-rays are collected on a cylindrical film at a distance
R
=60 mm from the sample.
2. Structure of the polymeric SB phase.
Figure 2a shows an oriented diffraction pattern of polymer P3,8 in the SB phase and figure 2b is
a schematic representation of this pattern. In the following, we shall try to use the information
given by this pattern in order to describe the structure of the polymeric SB phase.
-
Along the magnetic field direction (meridian), one can see a series of equidistant Bragg
reflections (a) : these are the reflections on the smectic layers. The analysis of the powder patterns show that these reflections are resolution limited. (The resolution of our apparatus is àq -* 10- 2 A - where q is the momentum transfer vector : q
=4 7T sin 0 / A). The smectic
period d is roughly equal to the length f of the side chains measured on Dreiding
stereomodels in an extended configuration [18]. (d
=30.1 Â for P3,8, d
=32.3 À for P4,8 and d
=33.0 A for P5,8). Therefore, no interdigitation can be detected.
Fig. 2. - (a) X-ray diffraction pattern of polymer P3,8 in the SB phase. ACuKo!
=1.54 Â, sample-film
distance : 60 mm, H is the magnetic field direction (meridian). (b) Schematic representation of figure 2a. (a) Bragg reflections on the smectic layers. (b) First (10) equatorial reflection of the 2D
hexagonal lattice (the two next ones 11 and 20 can be seen in Fig. 7a).
A first difference between the polymeric and the conventional SB phases consists in the
large number of meridional reflections that can be seen in the former case. We have shown
[20] that this large number is related to the distribution of the polymer backbones. We measured the intensities of the Bragg reflections on the layers and derived the projection of
the electron density profile along the director in the polymeric SB phase. We could localize the
polymer backbones in sublayers 6 À wide along the director between two adjacent sublayers
of mesogenic cores (Fig. 3) (see also Ref. [3]).
-
In the directions perpendicular to the meridian (equator), we find a series of 3 rather
sharp reflections (b), the first being by far the strongest (the two other ones can be seen in Fig. 7a). These equatorial reflections show that the layers are not liquid-like as in a SA or Sc phase but solid-like. The correspond to lattice spacings : 4.45 Â, 2.55 Á, 2.23 Â
which are in a ratio 1, 1/ J3, 1/ 4. They are the first spacings displayed by a 2D hexagonal
lattice of parameter a = 5.15 À. (The same value of a is obtained for P3,8, P4,g and P5,8. It is quite comparable to those found in the case of conventional SB phases [5] ; in particular it leads to a value of about 23 Â2 for the molecular area of a mesogenic core).
Another difference between the polymeric and conventional SB phases consists in the larger
number of equatorial reflections displayed by the former one. This suggests that the Debye
Waller factor of the polymeric SB phase should be smaller than that of the conventional
SB phase. This point will be considered later. Moreover, we do not detect, undemeath the 10 reflection, any diffuse ring which would be due to an amount of material still in the
SA phase. This SA phase plays here the role of the amorphous material in a usual polymeric crystal. Therefore, the amount of material still in the SA phase (i.e. not organized in the SB phase) is probably less than 5 %.
Fig. 3.
-Organization of the backbones along the director in the 83 phase [20] : the backbones are
squeezed in regions of width 6 Â along the director.
An analysis of the powder patterns shows that the equatorial reflections are not resolution limited. Figure 4 presents the microdensitometric profile of the 10 reflection compared to that
of the beam and to that of the SA equatorial diffuse crescent. The fact that the widths of the
equatorial reflections are not resolution limited may be explained in several ways. First let us consider the polymeric SB phase as a polymeric crystal : the width of a given reflection may be due to the juxtaposition of two close reflections, or to the small size of the crystallites or even
to a second order type of disorder. We can also compare the polymeric SB phase to the
conventional SB phase and the width of the 10 reflection will make us think that the polymeric
SB phase is of a hexatic nature rather than a crystal B. In the following, we shall examine the widths of the equatorial reflections according to these various possibilities.
-
We have first tried to account for the width of the 10 reflection by assuming the presence of a 101 3-dimensional reflection. Figure 5 shows that the experimental width of the 10 reflection cannot be explained by the presence of two 100 and 101 resolution limited reflections. (We have also checked that the experimental width cannot either be explained by varying the widths of these two reflections if they are kept equal.) Therefore, the 10 equatorial reflection is not broadened by a hypothetical 3-dimensional 101 reflection.
Fig. 4. Fig. 5.
Fig. 4.
-Intensity profiles (in arbitrary units) of : 1) the direct beam ; 2) the 10 equatorial reflection of the 2D hexagonal lattice in the polymeric SB phase ; 3) the equatorial diffuse ring in the SA phase. qo represents only the central value of each profile.
Fig. 5.
-Tentative deconvolution of the experimental 10 equatorial reflection (curve 1) into two hypothetical resolution limited 100 and 101 reflections (dashed lines). There is an obvious discrepancy
between curve 1) and curve 2) which represents the sum of the two hypothetical reflections.
- Then, the widths of the equatorial reflections may be due to the small size of the
crystallites. At this point, let us consider figure 6 which shows the X-ray diffraction pattern of the crystalline phase of a magnetically aligned sample of polymer P3,4 cooled from the
SA phase (the same type of pattern is observed in the case of polymer P4,4). This pattern shows
many additional reflections compared with that of P3,8 and can only be indexed in a 3- dimensional lattice. The equatorial reflections of these crystalline phases are not resolution
limited either, but nonetheless, they are all of the same width. Therefore, we can account for
this experimental width by the effect of the size of the crystallites : we estimate this size using
Scherrer’s formula [16] :
This leads to a value L
=150 Á. this size may also be interpreted as a typical distance
between defects.
However, in the case of the polymeric SB phase, a microdensitometric recording of the
reflections shows that the 11 reflection is nearly twice as wide as the 10 reflection. Therefore,
the widths of the equatorial reflections are not only braught about by the small size of the
crystallites.
b)
Fig. 6.
-(a) X-ray diffraction pattern of polymer P3,4 in the crystalline phase. ÀCuKa =
1.54 Á, sample-film distance : 60 mm. H is the magnetic field direction (meridian). (b) Schematic representation of figure 6a. (a) 00 f reflections. (b) hk 0 reflections. (c) hke reflections with h =1= 0, k =1= 0 and l= 0. The presence of these reflections (c) shows that the organization is 3-
dimensional here.
- Then, we may consider that the widths of the equatorial reflections are due to some
disorder of the second type (i. e. the polymeric SB phase is of a paracrystalline nature). Two neighbouring lattice vectors fluctuate independantly around their mean value : a. They are equal to a + Aa and their statistical distribution is characterized by the average square
(âa2). If we follow Hosemann’s point of view [22] that the reflections can still be detected for
(h 0394a2 > 1/2 )/a 0.3 and if we consider that the 30 reflection cannot be detected, then we
estimate (âa2) 1/2 = 0.7 A. (This last value is only an order of magnitude). Therefore, the
widths of the equatorial reflections can be explained by assuming that the distances between
neighbouring molecules fluctuate independantly by about 10 %.
The presence of a second type disorder does not exclude the existence of a first type disorder such as thermal agitation. To evaluate the part of first type disorder, i. e . to evaluate
the Debye Waller factor, it is necessary to measure the integrated intensities of the equatorial
reflections and to determine their dependance upon scattering angle. However, we only see
three orders of reflection and the last one does not allow a good determination of its
integrated intensity so that we shall go no further than stating that the Debye Waller factor of this polymeric SB phase must be smaller than that (2 B -- 20 [5] ) of a conventional
SB phase as mentioned previously.
Now, we can also compare the polymeric and conventional SB phases and first, we must
stress the following point : we do not detect either in figure 2a or on the powder patterns any hkl line with h # 0, k =F 0 and l # 0. As mentioned above, a hypothetical 3-dimensional 101 line close to the 10 reflection cannot be detected either. Since there is no evidence of any long
range 3D correlations then the polymeric SB phase should not be called crystal B and the packing of the mesogenic cores in 2-dimensional. For that reason, we also tried to explain the experimental width of the 10 reflection by assuming that within a layer, the 2D hexagonal
lattice is perfect and infinite but that the layers are completely uncorrelated. (We already used
a similar approach in a previous study of the conventional SF phase [23]). Under such assumptions, in the reciprocal space, the nodes of the hexagonal lattice become rods elongated along the meridian. The width of these rods is resolution limited and their length is
about 2/c A- 1. The diffracted intensity is obtained by projecting these rods on the Ewald
sphere. However these assumptions lead to a 10 reflection still much smaller than the
experimental one. Therefore the 2D hexagonal lattice of the mesogenic cores does not show a
true positional long range order. The absence of such a positional long range order is precisely
one of the characteristic features of the hexatic phase. Indeed, the width of the 10 reflection in the polymeric SB phase is à (2 0) = 0.75° which is comparable to that observed by Pindak
et al. [13] in the stacked hexatic SB phase of conventional mesogens. Consequently, it was tempting to try to fit the intensity profile of the 10 reflection along the equator with different theoretical curves. A fit of the wings of the reflection with a power law in q-
a[9] led to a
value : a - 1. 1 hard to account for except that it means that the structure could hardly been
considered a 3D crystal. A fit with a Lorentzian (awaited for a hexatic organization) was not satisfactory either. However, we must stress the fact that we do not have a true single domain
and then our intensity profile also integrates some intensity scattered in other diffuse areas
such as the diffuse spots described and called (b) in reference [9]. Furthermore, we may also
integrate a very small contribution due to a part of the material that would have kept a SA organization (the equivalent of the amorphous part of a polymeric crystal). On the other
hand, the revolution symmetry about the director of our samples prevents us from probing an
eventual long range orientational order characteristic of a stacked hexatic B phase.
Finally, we need to reconcile the two points of view of 2D paracrystal and stacked hexatic B
phase : as far as the correlations within a layer are concerned, the two approaches are similar except that the paracrystal theory only specifies the average square value of the fluctuations whereas the model of the stacked hexatic phase gives a detailed microscopic description of the organization and postulates that the reflection profile should be a Lorentzian curve. We could not reliably measure this profile and thus we failed to verify this Lorentzian dependance. As
far as the interlayer correlations are concerned, they are not relevant to the idea of a 2D paracrystal whereas they should be long range for the bond orientational order parameter as
was observed by Pindak et al. [13]. However, our lack of true monodomains of the polymeric SB phase did not allow us to probe such interlayer correlations and prevented us from obtaining a complete determination of the phase structure.
3. Fluctuations and local order in the polymeric SB phase.
Figure 7a shows an overexposed X-ray diffraction pattern of polymer P3,8 in the polymeric SB phase and figure 7b is a scheme of this pattern. One can see some intensity diffracted in four different types of diffuse areas : (c), (d), (e) and (f). In a first step, we shall describe these diffuse areas which are of two kinds :
-
some are diffuse spots much broader than those of the 2D hexagonal lattice located
around points of the X-ray diffraction pattern. Because of the fiber geometry of our sample, they correspond to the intersections with the Ewald sphere of a series of tori present in reciprocal space. The diffuse spots (c) are located in the equatorial plane around 1 q 1
=2 03C0 /3.4 Â - 1. By carefully inspecting them, we notice that they are slightly split off the equator. The diffuse spots (d) are aligned along rows parallel to the meridian and are located in the same planes as the 00 f Bragg spots. The diffuse spots (c) and (d) are of a different
nature as we shall see below but might be related in some way ;
-
some are diffuse lines on the X-ray diffraction pattern which correspond to the
intersection with the Ewald sphere of a series of planes in reciprocal space. The diffuse lines
(e) can be seen in the direction of the meridian to which they are perpendicular. They go
through the Bragg spots 00 1 towards the rows of diffuse spots (d). The diffuse lines (f) are
similar to the diffuse lines (e) in that they can also be seen in the direction of the meridian to
which they are perpendicular, in that they go through the first Bragg spots 001 and in that they
extend towards the rows of diffuse spots (d) on which they superimpose. They are different
from the diffuse lines (e) in that the closer they get to the diffuse spots (d), the more they tilt
with respect to the equator.
Fig. 7.
-(a) Overexposed X-ray diffraction pattern of polymer P3,8 in the SB phase. ACuKa
=1.54 Â, sample-film distance : 60 mm. H is the magnetic field direction (meridian). (b) Schematic representation of figure 7a : (a) reflections on the smectic layers ; the fact that their size increases with their order is only due to a slight mosaicity ; (b) 10, 11 and 20 equatorial reflections of the 2D hexagonal lattice ; (c) diffuse spot located along the equator around [ q 1
=2 ir/3.4 Â - 1. By carefully inspecting figure 7a, one can notice that this spot is slightly split off the equator ; (d) diffuse spots
«1/2 0 f
»located in the same planes as the 00 f Bragg spots. The
«1/2 0 5
»and
«1/2 0 6 » diffuse spots cannot be detected and the
«1/2 0 2
»diffuse spot can hardly be seen ; (e) diffuse lines going through the 003 and 004 Bragg spots and perpendicular to the meridian ; (f) diffuse lines starting from the 001 Bragg spots and extending towards the rows of diffuse spots (d).
In the following, we try to analyse all these elements (c), (d), (e) and (f) separately as they
arise from distinct and a priori weakly correlated disorders.
Let us start with the diffuse spots (c). They show that an additional short range order exists in the structure. Their wavevector q
=2 03C0 /3.4 Â- 1 is simply related to that of the hexagonal
lattice (3.4/4.45
=2/ J7). We have already observed [9] such diffuse spots on the X-ray
diffraction patterns of the conventional SB phase. Their positions in reciprocal space break the
hexagonal symmetry since they only present a rectangular symmetry : a 2D hexagonal lattice
may also be described by a centered rectangular lattice, the positions at the corners and at the
center of the cell being identical. The diffuse spots (c) show that locally, these two positions
are not equivalent any more (Fig. 8). Such an organization, called Herring bone array, extends only on a small distance, roughly l = 20 Â. (Actually, because of the fiber geometry of our samples, we have no direct evidence that the diffuse spots (c) indeed break the
symmetry of the 2D hexagonal lattice. We suppose that it is so because of the complete
analogy between these spots and those seen in reference [9].)
What is new in the polymeric SB phase is that, carefully inspecting figure 7a, we notice that
the diffuse spot (c) is slightly split off the equator. This splitting is large enough to be sure that
it is not due to the mosaicity of our sample. This means that the herring bone short range order is slightly correlated along the meridian. This feature was not observed in the case of conventional mesogens and we can see here the influence of the polymer backbone. A relative decrease (or even a complete cancellation) of the intensity of the diffuse spot (c) along the equator may be obtained by assuming the following arrangement of the mesogenic
cores : let us consider a mesogenic core in a given position of the herring bone lattice (say at
the center of the rectangular cell for instance), we assume that, statistically, the mesogenic
cores located just below and above the first one in the adjacent layers occupy the other
position of the lattice (here, the corner of the rectangular cell). (See Fig. 9) Projected on the equatorial plane, the rectangular lattice turns back to the initial hexagonal one. In that case, if
these correlations were perfect, the intensity of the diffuse spot (c) on the equator should be cancelled. However, since this intensity is still important, then these longitudinal correlations
are weak. From the extension of the diffuse spots (c) along the meridian, we deduce that these correlations are short range, limited to the nearest neighbours in the adjacent layers. Here, the influence of the polymer tacticity should be important.
Fig. 8. Fig. 9.
Fig. 8.
-Herring bone array fluctuations [9] in the 2D hexagonal lattice. (x) nodes of the 2D hexagonal
lattice. Three rectangular cells have been represented which show the three possible orientations of the
herring bone array fluctuations with respect to the 2D hexagonal lattice.
Fig. 9.
-Herring bone lattice correlations along adjacent layers. Solid lines : molecular sections of the
mesogenic cores in a given layer. Dashed lines : molecular sections of the mesogenic cores in the two adjacent layers.
Let us now turn to the diffuse spots (d) : they are aligned along rows parallel to the
meridian in figure 7a. These rows of diffuse spots correspond to the intersection with the Ewald sphere of a series of tori. These tori have the meridian for axis and are located in the
same planes as the 00 f Bragg spots. The component of their wave vector along the equator is roughly half of that of the 10 reflection of the 2D hexagonal lattice. (We shall discuss this
point later.) Therefore, in the following, we shall denote these diffuse spots
«1/2 0 f
»to
remind that they are located in the same planes as the 00 l Bragg spots.
These diffuse spots were already observed on the X-ray patterns of P3,8, P4,8 and P5,8 in the SA phase but with a lesser contrast. They are similar to those already observed on
the X-ray patterns of a mesomorphic side chain polymethacrylate [24]. They were interpreted by the existence of a purely displacive transverse modulation, i.e. to undulations of the layers.
In the case of the polymethacrylate described in reference [24], only one diffuse spot could be detected. Conversely, in the present case a whole series of diffuse
«1/2 0 f
»can be seen.
However, we do not see the
«1/2 0 5
»and
«1/2 0 6
»diffuse spots. Moreover, the intensity
ratios of the diffuse spots
«1/2 0 3 »/« 1/2 0 1
»and
«1/2 0 4 »/« 1/2 0 1
»is much larger than
those of the Bragg spots 003/001 and 004/001. (The intensity of the first diffuse spot is hard to evaluate because of the presence of the diffusion (f) which superimposes itself and displaces
the maximum. However, taking this effect into account should decrease even more the
intensity of the
«1/2 0 1
»diffuse spot relatively to the others.) These remarks show that, in opposition to those of the Bragg spots, the intensities of the diffuse spots (d) do not simply
follow the structure factor variation along the meridian.
We can qualitatively account for these facts by using the model developed in reference [24].
Let us assume a sinusoidal transverse displacement of the layers of amplitude uz, then the
integrated intensity of the various «1/20l» spots will vary as Jf(zrfuz/c) where
JI is the Bessel function of order 1. If we now consider that a smectic layer undulates as a whole, then the integrated intensity of the
«1/2 0 1
»spots will be described by the product :
Jf( ’TTeuz/c) x fool where fool is the structure factor of the 00 f Bragg reflection measured in reference [9]. Figure 10 shows the function Jf( zrfuz/c ) with uz = 3 A ; this function will be maximum for 3, l=4 and close to zero forl = 5, l = 6 in good agreement with the experimental results.
Fig. 10.
-Function Jf( ’TT f uz/ c). JI is the 1 st order Bessel function. f is (2 d / À ) sin 0 which on a diffuse
spot
«1/2 0 f
»is simply its order of reflection. (+) values of the function J;( ’TTfuz/ c) for each reflection.
(.) integrated intensity of the diffuse spots : J;(’TTfuz/c) x fool.
Therefore, the diffuse spots can be interpreted as undulations of the layers, without distortion, of amplitude approximately 3 Â. This value is in fair agreement with the width
(6 ± 1 Â ) of the region of backbones found in the projection of the electron density along the
director [20]. The coherence length along the equator of this short range order, derived from
the extension of the diffuse spots (d) is roughly 20 Â.
The presence of the diffuse line (f) prevents us from measuring the
«1/2 0 0
»diffuse spot
(on the equator) if it exists. Therefore, it is not quite sure whether the distortion which gives
rise to the row of diffuse spots (d) is purely displacive or not and then whether our model fully
describes it or not.
At this point, it should be noted that other examples of various orders coexisting with a 2D hexagonal lattice may be found in the existing literature about the structures of liquid crystals.
Leadbetter et al. [25, 26] have observed some satellites around the 001 Bragg spot in the SB phase of some conventional mesogens. They were shown to arise from undulations of the smectic layers. However these undulations are quite different from those observed in the present case because the former ones are pretransitional effects related to the existence of a
SH phase below the SB phase. Furthermore, their period was approximately 80 Â indepen- dantly of the compound studied and in no way related to the hexagonal lattice.
A relation between a 2D hexagonal order and an antiferroelectric order has already been
shown in the hexatic phase of a polar mesogen [27]. However, in that case, the two types of order were incommensurate as the antiferroelectric order did not couple itself strongly with
the hexatic lattice. Moreover, the antiferroelectric order correlation length was about ten
times larger than that of the layer undulations described above.
The origin of the undulations of the layers may be explained [24] either by a reaction of the
backbones to their confinement imposed by the smectic field or by a difference between the
grafting density and the packing density of the mesogenic cores which imposes a local splay configuration to the spacers. Anyway, the polymeric nature of the compound plays an important role in the origin of the undulations, the period of which is determined by the packing and elastic properties of the system. Thus, the period of these undulations measured in reference [24] and also in the SA phase of polymers P3,8, P4,8 and P5,8 is roughly
20 ± 5 Á. The interaction of these undulations with the 2D hexagonal order decreases this value to roughly 9 A (a ~3= 9 À ) which is about twice the distance between the simplest
and densest planes (10) of the 2D hexagonal lattice. We can illustrate this effect by adopting
the following image (Fig. 11 ) : the presence of the extremity by which the mesogenic core is grafted on the backbone allows us to define an
«up
»or
«down
»direction for the mesogenic
core, similar to the direction of the dipole of a polar mesogen. On the molecular scale, a coupling between this direction and the undulations may exist : the mesogenic cores may
Fig. 11.
-Coupling between the layer undulations and the 2D hexagonal lattice. (+) mesogenic cores
displaced in the direction of c. (e) mesogenic cores displaced in the direction opposite to c.
alternately point upwards when they are displaced along the meridian in one direction (say
+ z) and downwards in the other (say - z). Since our samples present a fiber geometry, we
cannot determine the local symmetry of the undulations ; in particular, we cannot experimentally choose between rectangular and hexagonal symmetries. However, the
undulations which consist in displacing a mesogenic core along + z and its neighbour along
-