 Nano Express
 Open Access
 Published:
Disorder to Order Transition and Ordered Morphology of CoilComb Block Copolymer by SelfConsistent Field Theory
Nanoscale Research Letters volume 10, Article number: 328 (2015)
Abstract
The disorder to order transition and the ordered patterns near the disordered state of coilcomb copolymer Ab(B_{ m + 1}gC_{ m }) are investigated by the selfconsistent field theory. The phase diagrams of coilcomb copolymer are obtained by varying the composition of the copolymer with the side chain number m = 1, 2, and 3. The disorder to order transition is far more complex compared with the comb copolymer or linear block copolymer. As the side chain number m increases, the FloryHuggins interaction parameter of disorder to order transition (DOT) increases and the lowest DOT occurs when the volume fractions of blocks A, B, and C are approximately equal. When one component is the minority, the disorder to order transition curve is similar with binary copolymer, but the curve shows the asymmetric property. The comb copolymer is more stable with larger side chain number m and shorter side chain. The ordered patterns from the disordered state are discussed. The results are helpful for designing coilcomb copolymers and obtaining the ordered morphology.
Background
The ability of block copolymers to spontaneously form microphaseseparated structures with length scales of 10–100 nm indeed makes them extensive applications in nanoscience, such as pore materials [1], drug delivery [2], and templates [3, 4]. Recently, researchers are devoted to design block copolymers with different architectures to engineer functional materials. Even the crystal structures of block copolymers [5–9] were intensively studied. For example, the FrankKasper σ phase can form in two different singlecomponent, sphereforming, block copolymer melts near the orderdisorder transition temperature (T _{ODT}) [6, 7]. Xie et al. [8] studied asymmetric miktoarm block copolymers which can selfassemble into fcc, bcc, A15, and the complex σ phase. They even designed multiblock terpolymers which can selfassemble into various binary mesocrystals with space group symmetries of a large number of binary ionic crystals, including NaCl, CsCl, ZnS, αBN, AlB_{2}, CaF_{2}, TiO_{2}, ReO_{3}, Li_{3}Bi, Nb_{3}Sn(A15), αAl_{2}O_{3}, etc. [9]. This study showed that block copolymer with different architectures can be used to obtain the complex nanostructures or even construct crystal phase by macromolecular metallurgy in a mesoscale.
Coilcomb copolymers, which selfassemble at a length scale of a few nanometers, can be constructed by attaching oligomers or small molecules to polymers via covalent bond and noncovalentbonding interactions, for example, hydrogen bonding, electrostatic interactions, or metal coordination [1, 3, 4, 10–27]. They have potential applications such as in electrical, biological, and other functional materials. Feng et al. [12–14] focused on double hydrophilic coilcomb copolymer, in which the side chain grafted to the backbone through covalent bond. And they found its potential applications in templates and biological materials. Ten Brinke and coworkers [3, 4, 16–21, 26] reported a series of Ab(B_{ m + 1}gC_{ m }) coilcomb copolymers, where the small molecules C are weakly connected to backbone B through hydrogen bonds, and the coilcomb copolymers can selfassemble into hierarchically ordered structures. In these structures, there were two different length scales: the larger length scale period is mainly driven by the separation between the comb part and the coil part, whereas the small length period is produced by the segregation within the comb part.
Besides, some researchers also found these hierarchically ordered structures of coilcomb copolymer based on theoretical simulation [28, 29]. For instance, by using the realspace implemented selfconsistent field theory, Wang et al. [29] reported that the coilcomb block copolymers exhibit hierarchically ordered microstructures, including parallel and perpendicular lamellawithinlamella, cylinderwithinlamella, lamellawithincylinder, and cylinderwithincylinder.
The ordered phase can form when the repulsive interaction parameter χN is larger than the interaction parameter of the disorder to order transition. Therefore, it is very important to determine the disorder to order transition of block copolymers. It can help us to find ordered microstructures easily. Therefore, more and more researchers pay attention to the disorder to order phase transition of supramolecular polymers [30–32]. At the meantime, selfconsistent field theory (SCFT) method has been largely used to study the phase behavior of block copolymers [33–37]. It is also used to study the disorder to order transition of block copolymers [38, 39]. Even the SCFT method has been used to successfully study the polydispersityinduced disorder to order transition of block copolymers [33, 40–42]. In this work, we consider the disorder to order transition of coilcomb copolymer Ab(B_{ m + 1}gC_{ m }) with different side chain numbers by using the SCFT. Due to the complexity of this copolymer, we only consider the stability of the homogeneous phase relative to the microseparated state. The related parameters are the side chain number m, the volume fraction of blocks A, B, and C, and the FloryHuggins parameter χN. We construct the phase diagram of disorder to order transition of coilcomb copolymer by continuously varying the composition of the block copolymer.
Methods
We consider n comb copolymers Ab(B_{ m + 1}gC_{ m }) with polymerization N in a volume V and there are m branching points (or the side chain number) along the main chain B, which divide the B chain as m + 1 equal parts (we called it “divided sections”) with polymerization N _{B} and each side chain C has N _{C} segments for block C, respectively. So, N = N _{A} + (m + 1)N _{B} + mN _{C}. The schematic diagram of a comb copolymer molecule is presented in Fig. 1. The monomers of the main chain and the side ones are assumed to be flexible with a statistical length a. Therefore, the compositions (average volume fractions) are f _{A} = N _{A}/N, f _{B} = (m + 1)N _{B}/N, f _{C} = 1 − f _{A} − f _{B} for blocks A, B, and C, respectively.
Due to the different architectures of blocks A, B, and C, we define six distribution functions, i.e., q _{A}(r, s) and q _{A} ^{+}(r, s), q _{B}(r, s, t) and q _{B} ^{+}(r, s, t), and q _{C}(r, s) and q _{C} ^{+}(r, s, t) where s is the contour along the main chain for AB and along the side chain for C, t is the number along the block B of main chain AB divided by the side chains C, and it belongs to [1, m + 1]. With these definitions, the polymer segment probability distributions q and q ^{+} for main chain AB and side chain C satisfy the modified diffusion equations:
where w is w _{A} when s belongs to block A, w _{B} when belongs to block B, and w _{C} when belongs to block C. The initial conditions are q _{C}(r, 0) = 1, q _{A}(r, 0) = 1, q _{B}(r, 0, 1) = q _{A}(r, N _{A}), q _{B}(r, 0, t) = q _{B}(r, N _{B}, t − 1)q _{C}(r, N _{C}) for t > 1, q _{B} ^{+}(r, N _{B}, m + 1) = 1, q _{B} ^{+}(r, N _{B}, t) = q _{B} ^{+}(r, 0, t + 1)q _{C}(r, N _{C}) for t < m + 1, q _{C} ^{+}(r, N _{C}, t) = q _{B}(r, N _{B}, t)q _{B} ^{+}(r, 0, t + 1), q _{A} ^{+}(r, N _{A}) = q _{B} ^{+}(r, 0, 1), where t∈ [1, m]. Accordingly, the partition function of a single chain subject to the mean field w _{ i }, where i represents block species A, B, and C, can be written as Q = ∫d r q _{B}(r, N _{B}, m + 1).
With the above description, the free energy function (in units of k _{ B } T) of the system is given by:
where χ _{ ij } is the FloryHuggins interaction parameter between different species (i, j = A, B, C, i ≠ j), ϕ _{ i } is the monomer density of each species (i = A, B, C), and ξ is the Lagrange multiplier (as a pressure).
Minimization of the free energy to mean field, density, and pressure, δF/δw = δF/δϕ = δF/δξ = 0, leads to the following selfconsistent field equations that describe the equilibrium state:
Here, we solve Eqs.(4)–(10) directly in real space by using a combinatorial screening algorithm proposed by Drolet and Fredrickson [43, 44]. Note that one must solve the diffusion equation first for q _{C}(r, s) and q _{A}(r, s) with initial condition q _{C}(r, 0) = 1 and q _{A}(r, 0) = 1, then for q _{B}(r, s, t) with q _{B}(r, 0, 1) = q _{A}(r, N _{A}), q _{B}(r, 0, t) = q _{C}(r, N _{B}, t − 1)q _{C}(r, N _{C}) for t > 1 and for q _{B} ^{+}(r, s, t) with q _{B} ^{+}(r, N _{B}, m + 1) = 1, q _{B} ^{+}(r, N _{B}, t) = q _{B} ^{+}(r, 0, t + 1)q _{C}(r, N _{C}) for t < m + 1, and last for q _{C} ^{+}(r, s, t) and q _{A} ^{+}(r, s) with q _{C} ^{+}(r, N _{C}, t) = q _{B}(r, N _{B}, t)q _{B} ^{+}(r, 0, t + 1) and q _{A} ^{+}(r, N _{A}) = q _{B} ^{+}(r, 0, 1). Each iteration continues until the phases are stable. Several times are repeated by using different initial conditions to avoid the trapping in a metastable state. In addition, we also minimize the free energy with respect to the system size because it has been pointed out that the box size can influence the morphology [45]. The implementation of the selfconsistent field theory is carried out in a twodimensional L _{ x } × L _{ y } lattice with periodic boundary conditions.
We consider the disorder to order transition with different side chain numbers m and the ordered pattern near the disorder to order transition. In our calculation, we consider the condition: symmetrical interaction parameters χ _{AB} N = χ _{AC} N = χ _{BC} N = χN. Thus, we calculate the crossover curve of the disordered phase and an (unspecified) ordered phase in terms of the normalized FloryHuggins parameter χN, the relative composition, and the number of teeth in the comb m. By systematically changing the volume fractions of A, B, and C blocks, we can construct the component triangle phase diagrams in the entire range of the copolymer composition.
Results and Discussion

a.
Phase diagrams of disorder to order transition for Ab(B_{ m + 1}gC_{ m }) (m = 1–3)
In this part, we only consider the cases for comb side chain number m = 1, 2, and 3, and the interaction parameters between each block are set to be equal: χ _{AB} N = χ _{AC} N = χ _{BC} N = χN. Besides, the chain length is N = 120 for these three cases. By systematically varying the volume fractions of the three blocks (f _{A}, f _{B}, and f _{C}) and the FloryHuggins parameter χN, we got the phase diagrams of the disorder to order transition for the coilcomb copolymer, which are shown in Fig. 2, and parts a, b, and c are referred to the situations of m = 1, 2, and 3, respectively. According to the figure, we can find that the disorder to order transition (DOT) parameter χN is larger at the corners of the three blocks, and the χN of DOT is lower when the volume fractions of the three blocks are approximately comparable. By comparing these three figures, we also can see that with the increasing of comb side chain number m, the χN of DOT increases largely, which corresponds to the lower temperature to microphase separate, i.e., the system becomes more stable. We can see that the χN of DOT is larger when the coilcomb copolymer has the longer block B or longer block C. This result is different from our previous research on the DOT of A_{ m + 1}(BC)_{ m } [46] because the topological structure between these two kinds of copolymer is different. In this condition, block A is much free and only one end is confined by block B, while blocks B and C are much restricted by the junctions.
Besides, we also got the phase diagrams when the volume fractions are f _{A}, f _{B}, f _{C} = 0.1, which are shown in Fig. 3, respectively. We can find that when the volume fraction f _{A}, f _{B}, or f _{C} is small, the diagrams are similar with those of diblock copolymer, which also has a minimum of χN in the phase diagram. When f _{A} is small, as shown in Fig. 3 (a1), (b1), (c1), the topological structure of copolymer becomes comblike, and the sections of blocks B and C are restricted by each other. However, block B is also restricted by block A. So, the influence of block B on DOT is larger than that of block C. Compared with the comb block copolymer (B_{ m + 1}gC_{ m }) [37], we can see that the disorder to order transition is very similar. The curves are asymmetric. When f _{B} is small, from Fig. 3 (a2), (b2), (c2), we can see that with the increase of the side chain number m, the gap between the χN of ends in the diagram is much larger. Because with the increase of the side chain number m, more segments of block C are restricted, while the length of block A is still fixed and relatively free, which means the influence of block A on the DOT is smaller than that of block C. Based on Fig. 3 (a3), (b3), (c3), we can get the similar conclusion for the situation when f _{C} is small. According to the above analysis, we conclude that block A can separate from the copolymer first, then block C and last block B, which are determined by the topological structure of the copolymer. From Figs. 2 and 3, we can see that the confined segments increase with the increase of the side chain number, so the χN increases, which means the lower temperature of microphase separation.

b.
Disorder to order transition for Ab(B_{ m + 1}gC_{ m }) when fixing blocks A, B, and C
If we fix the length of the three sections (block A, block B, and side chain C), the interaction parameters of disorder to order transition vary with the increase of the side chain number m. Figure 4 shows the interaction parameters of disorder to order transition χ _{DOT} N of coilcomb copolymer Ab(B_{ m + 1}gC_{ m }) for two cases: (1) N _{A} = 15, N _{B} = 5, N _{C} = 10(squares) and (2) N _{A} = 85, N _{B} = 5, N _{C} = 10(spheres), where the x coordinate is represented by the volume fraction of block A converted by f _{A} = N _{A}/(N _{A} + (m + 1)N _{B} + mN _{C}). When the volume fraction of coil part (block A) is less than 0.5, the χ _{DOT} N increases with the increase of the side chain number m. But when the volume fraction of coil part (block A) is more than 0.5, the χ _{DOT} N decreases with the increase of the side chain number. From the figure, we can see that the χ _{DOT} N is relatively low when f _{A} is near to 0.5, while the χ _{DOT} N increases when f _{A} is far from 0.5 by varying the side number m of the comb part.

c.
Ordered pattern near the disorder to order transition
Ordered Morphology
Based on the phase diagrams of the disorder to order transition, we also predicted the ordered pattern near the disorder to order transition. Several times are repeated by using different initial conditions to avoid the trapping in a metastable state. In addition, we also minimize the free energy with respect to the system size because it has been pointed out that the box size can influence the morphology. From the ordered pattern, we can clearly see the selfassembly structure of the coilcomb block copolymer. Here, we only present the phase diagrams for symmetrical interaction parameters, i.e., χ _{AB} N = χ _{AC} N = χ _{BC} N = χN. We only consider the side chain number m = 1–3.
Figure 5 shows the ordered patterns near the disorder to order transition for m = 1–3. The stable morphologies are twocolor lamella (LAM_{2}), hexagonal phase (HEX), coreshell hexagonal phase (CSH), two interpenetrating tetragonal phase (TET_{2}), hexagonal lattice outside coreshell hexagonal phase (CSH_{2}), and hexagonal lattice outside hexagonal phase (HEX_{2}).
Phase Diagram Based on the Ordered Pattern Near DOT
Comparing with the morphologies of coilcomb copolymer at larger χN [36], less morphologies occur near the disorder to order transition. Figure 6 presents the phase diagram based on the ordered pattern near DOT for coilcomb copolymer with teeth m = 1, 2, and 3. For m = 1, there are five ordered morphologies near the disordered state. They are LAM_{2}, HEX, CSH, TET_{2}, and CSH_{2}. The morphologies are simple compared with those at larger interaction parameters. Near the three corners, the ordered phase is hexagonal (HEX or CSH). When one of the components is minority, the phase behavior is similar to that for diblock copolymer. But, when the three components are comparable, the stable phase is CSH, which is different from diblock copolymers. The complex phases, such as TET_{2} and CSH_{2}, emerge near the disordered state. Here, we can see that near the corner C, the stable phase is CSH_{2}, while the stable phase near the other two corners A and B is HEX. This result shows that longer block C easily separates from block B. The coil part (block A) can spontaneously separate from the comb part. Therefore, the coreshell hexagonal phase forms. Near the disorder to order transition, the lamellar phase is only two colored.
For m = 2, the phase diagram is similar with that for m = 1. But the region of hexagonal phase (HEX and CSH) enlarges. Another new phase (CSH_{2}) occurs, and the phase TET_{2} for m =1 does not appear here. For m = 3, there are four stable phases. The complex phase CSH_{2} does not occur here, and the phase region of CSH phase enlarges. Comparing the three phase diagrams, we can see that the effect of the comb part becomes strong with the increase of the side chain number of the comb part. When the coil part block A is the minority, the phase separation of the coilcomb block copolymer is complex. The separation between the coil and comb part is natural. The separation between the main chain and the side chain will compete with the separation between the coil and comb part; therefore, the complex phases (TET_{2}, CSH_{2}, HEX_{2}) form.
Conclusions
The disorder to order transition and the ordered patterns from the disordered state of coilcomb copolymer Ab(B_{ m + 1}gC_{ m }) are investigated by the selfconsistent field theory. The phase diagrams of coilcomb copolymer are obtained by varying the composition of the copolymer with the side chain number m = 1, 2, and 3. The disorder to order transition is far more complex compared with the comb copolymer or linear block copolymer. As the side chain number m increases, the FloryHuggins interaction parameter of disorder to order transition (DOT) increases and the lowest DOT occurs when the volume fractions of blocks A, B, and C are approximately equal. When one component is the minority, the disorder to order transition curve is similar with binary copolymer, but the curve shows the asymmetric property. The comb copolymer is more stable with larger side chain number m and shorter side chain. There are six ordered phases near the DOT: twocolor lamellar phase (LAM_{2}), hexagonal phase (HEX), coreshell hexagonal phase (CSH), two interpenetrating tetragonal phase (TET_{2}), hexagonal lattice outside coreshell hexagonal phase (CSH_{2}), and hexagonal lattice outside hexagonal phase (HEX_{2}). The results are helpful for designing coilcomb copolymers and obtaining the ordered morphology.
References
MakiOntto R, de Moel K, de Odorico W, Ruokolainen J, Stamm M, ten Brinke G, et al. “Hairy tubes”: mesoporous materials containing hollow selforganized cylinders with polymer brushes at the walls. Adv Mater (Weinheim, Ger). 2001;13:117–21.
Ahmed F, Discher DE. Selfporating polymersomes of PEGPLA and PEGPCL: hydrolysistriggered controlled release vesicles. J Controlled Release. 2004;96:37–53.
van Zoelen W, Bondzic S, Landaluce TF, Brondijk J, Loos K, Schouten AJ, et al. Nanostructured polystyreneblockpoly(4vinyl pyridine)(pentadecylphenol) thin films as templates for polypyrrole synthesis. Polymer. 2009;50:3617–25.
van Zoelen W, Vlooswijk AHG, Ferri A, Andringa AM, Noheda B, ten Brinke G. Ordered arrays of ferroelectric nanoparticles by pulsed laser deposition on PSbP4VP(PDP) supramoleculebased templates. Chem Mater. 2009;21:4719–23.
Bates FS, Hillmyer MA, Lodge TP, Bates CM, Delaney KT, Fredrickson GH. Multiblock polymers: panacea or Pandora’s box? Science. 2012;336:434–40.
Lee S, Bluemle MJ, Bates FS. Discovery of a FrankKasper sigma phase in sphereforming block copolymer melts. Science. 2010;330:349–53.
Lee S, Leighton C, Bates FS. Sphericity and symmetry breaking in the formation of FrankKasper phases from one component materials. Proc Natl Acad Sci U S A. 2014;111:17723–31.
Xie N, Li W, Qiu F, Shi AC. Sigma formed in conformationally asymmetric ABtype block copolymers. Acs Macro Letters. 2014;3:906–10.
Xie N, Liu M, Deng H, Li W, Qiu F, Shi AC. Macromolecular metallurgy of binary mesocrystals via designed multiblock terpolymers. J Am Chem Soc. 2014;136:2974–7.
Wang WJ, Liu R, Li ZY, Meng CF, Wu Q, Zhu FM. Synthesis and selfassembly of new doublecrystalline amphiphilic polyethyleneblockpoly[oligo(ethylene glycol) methyl ether methacrylate] coilbrush diblock copolymer. Macromol Chem Phys. 2010;211:1452–9.
Xu F, Li TC, Xia JF, Qiu F, Yang YL. (Polystyrenegpolyisoprene)bpolystyrene combcoil block copolymer in selective solvent. Polymer. 2007;48:1428–34.
Feng C, Shen Z, Gu LN, Zhang S, Li LT, Lu GL, et al. Synthesis and characterization of PNIPAMb(PEAgPDEA) double hydrophilic graft copolymer. J Polym Sci Pol Chem. 2008;46:5638–51.
Feng C, Shen Z, Li YG, Gu LN, Zhang YQ, Lu GL, et al. PNIPAMb(PEAgPDMAEA) doublehydrophilic graft copolymer: synthesis and its application for preparation of gold nanoparticles in aqueous media. J Polym Sci Pol Chem. 2009;47:1811–24.
Feng C, Li YJ, Yang D, Li YG, Hu JH, Zhai SJ, et al. Synthesis of welldefined PNIPAMb(PEAgP2VP) double hydrophilic graft copolymer via sequential SETLRP and ATRP and its “schizophrenic” micellization behavior in aqueous media. J Polym Sci Pol Chem. 2010;48:15–23.
Seo M, Shin S, Ku S, Jin S, Kim JB, Ree M, et al. Surfaceindependent vertical orientation of cylindrical microdomains in block copolymer thin films directed by combcoil architecture. J Mater Chem. 2010;20:94–102.
Ruokolainen J, Makinen R, Torkkeli M, Makela T, Serimaa R, ten Brinke G, et al. Switching supramolecular polymeric materials with multiple length scales. Science. 1998;280:557–60.
Ikkala O, ten Brinke G. Functional materials based on selfassembly of polymeric supramolecules. Science. 2002;295:2407–9.
van Ekenstein GA, Polushkin E, Nijland H, Ikkala O, ten Brinke G. Shear alignment at two length scales: combshaped supramolecules selforganized as cylinderswithinlamellar hierarchy. Macromolecules. 2003;36:3684–8.
Ten Brinke G, Ikkala O. Smart materials based on selfassembled hydrogenbonded combshaped supramolecules. Chem Rec. 2004;4:219–30.
Ikkala O, ten Brinke G. Hierarchical selfassembly in polymeric complexes: towards functional materials. Chem Commun (Cambridge, U K). 2004;7:2131–7.
Ruotsalainen T, Turku J, Hiekkataipale P, Vainio U, Serimaa R, ten Brinke G, et al. Tailoring of the hierarchical structure within electrospun fibers due to supramolecular combcoil block copolymers: polystyreneblockpoly(4vinyl pyridine) plasticized by hydrogen bonded pentadecylphenol. Soft Matter. 2007;3:978–85.
Kao J, Tingsanchali J, Xu T. Effects of interfacial interactions and film thickness on nonequilibrium hierarchical assemblies of block copolymerbased supramolecules in thin films. Macromolecules. 2011;44:4392–400.
Lee CH, Tung SH. Microdomain control in block copolymerbased supramolecular thin films through varying the grafting density of additives. Soft Matter. 2011;7:5660–8.
Tung SH, Kalarickal NC, Mays JW, Xu T. Hierarchical assemblies of blockcopolymerbased supramolecules in thin films. Macromolecules. 2008;41:6453–62.
Bondzic S, Polushkin E, Ruokolainen J, ten Brinke G. SAXS study of the lamellarcylindrical transition in the PIbMP(OG) supramolecules’ system. Polymer. 2008;49:2669–77.
de Moel K, van Ekenstein GORA, Nijland H, Polushkin E, ten Brinke G, MakiOntto R, et al. Polymeric nanofibers prepared from selforganized supramolecules. Chem Mater. 2001;13:4580–3.
Li WK, Liu SQ, Deng RH, Zhu JT. Encapsulation of nanoparticles in block copolymer micellar aggregates by directed supramolecular assembly. Angew Chem, Int Ed. 2011;50:5865–8.
Huang CI, Lin YC. Hierarchical structurewithinstructure morphologies in Ablock(BgraftC) molecules. Macromol Rapid Commun. 2007;28:1634–9.
Wang LQ, Lin JP, Zhang LS. Hierarchically ordered microstructures selfassembled from combcoil block copolymers. Langmuir. 2009;25:4735–42.
Tsao CS, Chen HL. Concurrent transformation of copolymer domain morphology induced by the orderdisorder transition of comb block in supramolecular combcoil block copolymer. Macromolecules. 2004;37:8984–91.
ten Brinke G, Huh J, Ruokolainen J, Torkkeli M, Serimaa R, Ikkala O. Orderdisorder transitions in comblike polymersurfactant systems involving hydrogen bonds. Macromol Symp. 1997;114:229–36.
Cortese J, SoulieZiakovic C, Cloitre M, TenceGirault S, Leibler L. Orderdisorder transition in supramolecular polymers. J Am Chem Soc. 2011;133:19672–5.
Sides SW, Fredrickson GH. Continuous polydispersity in a selfconsistent field theory for diblock copolymers. J Chem Phys. 2004;121:4974–86.
Jiang Z, Xu C, Qiu YD, Wang X, Zhou D, Xue G. Complex microstructures of ABC triblock copolymer thin films directed by polymer brushes based on selfconsistent field theory. Nanoscale Res Lett. 2014;9:359.
Tang P, Qiu F, Zhang HD, Yang YL. Morphology and phase diagram of complex block copolymers: ABC linear triblock copolymers. Phys Rev E. 2004;69:031803ss.
Wang R, Jiang Z, Yang H, Xue G. Side chain effect on the selfassembly of coilcomb copolymer by selfconsistent field theory in two dimensions. Polymer. 2013;54:7080–7.
Wang R, Jiang ZB, Hu JL. Order to disorder transition of comb copolymer A_{ m+1} B_{ m }: a selfconsistent field study. Polymer. 2005;46:6201–7.
Kumar R, Muthukumar M. Microphase separation in polyelectrolytic diblock copolymer melt: weak segregation limit. J Chem Phys. 2007;126:214902.
Lefebvre MD, de la Cruz MO, Shull KR. Phase segregation in gradient copolymer melts. Macromolecules. 2004;37:1118–23.
Wang YQ, Li XA, Tang P, Yang YL. Dynamics and orderdisorder transitions in bidisperse diblock copolymer blends. Physica BCondensed Matter. 2011;406:1132–8.
Beardsley TM, Matsen MW. Effects of polydispersity on the orderdisorder transition of diblock copolymer melts. Eur Phys J E. 2008;27:323–33.
Cooke DM, Shi AC. Effects of polydispersity on phase behavior of diblock copolymers. Macromolecules. 2006;39:6661–71.
Drolet F, Fredrickson GH. Combinatorial screening of complex block copolymer assembly with selfconsistent field theory. Phys Rev Lett. 1999;83:4317–20.
Drolet F, Fredrickson GH. Optimizing chain bridging in complex block copolymers. Macromolecules. 2001;34:5317–24.
BohbotRaviv Y, Wang ZG. Discovering new ordered phases of block copolymers. Phys Rev Lett. 2000;85:3428–31.
Qian Z, Wang R. Disordertoorder transition of triblock comb copolymer A_{ m+1}(BC)_{ m }. Macromolecules. 2011;44:6113–20.
Acknowledgements
This work was financially supported by the National Natural Science Foundation of China (grant nos. 21474051, 21074053 and 51133002) and Program for Changjiang Scholars and Innovative Research Team in University (PCSIRT). The numerical calculations in this paper have been done on the IBM Blade cluster system in the High Performance Computing Center (HPCC) of Nanjing University.
Author information
Authors and Affiliations
Corresponding author
Additional information
Competing Interests
The authors declare that they have no competing interests.
Authors’ Contributions
ZBJ, ZYQ, and HY carried out the simulations. ZBJ and ZYQ performed the data analysis and drafted the manuscript. ZBJ and RW participated in the design of the study and conceived of the study. All authors read and approved the final manuscript.
Rights and permissions
Open Access This article is distributed under the terms of the Creative Commons Attribution 4.0 International License (http://creativecommons.org/licenses/by/4.0/), which permits unrestricted use, distribution, and reproduction in any medium, provided you give appropriate credit to the original author(s) and the source, provide a link to the Creative Commons license, and indicate if changes were made.
About this article
Cite this article
Jiang, Z., Qian, Z., Yang, H. et al. Disorder to Order Transition and Ordered Morphology of CoilComb Block Copolymer by SelfConsistent Field Theory. Nanoscale Res Lett 10, 328 (2015). https://doi.org/10.1186/s1167101510358
Received:
Accepted:
Published:
DOI: https://doi.org/10.1186/s1167101510358
Keywords
 Coilcomb block copolymer
 Disorder to order transition
 Phase separation
 Selfconsistent field theory