Two PBTPA homopolymers with different molecular weight (PBTPA-L; M_n = 3700, and PBTPA-H; M_n = 6400) were synthesized via palladium-catalyzed C-N coupling polymerization [5] . The number average molecular weight (M_n) was determined by an end-group analysis with ¹H-NMR. Poly(methyl methacrylate) (PMMA) was prepared by an anionic polymerization as described elsewhere [24] . The block copolymer PBTPA-b-PMMA with the number average molecular weight of 8500 (PBTPA; M_n = 4300, PMMA; M_n = 4200) was synthesized by the combination of C-N coupling polymerization and atom transfer radical polymerization (ATRP) of MMA as follows. At first bromo ester terminated macroinitiotor PBTPA-MI (M_n = 4300) was prepared as described elsewhere [7] . Then ATRP of MMA was carried out.

A 5-mL flask equipped with a magnetic stirrer and a nitrogen inlet was charged with PBTPA-MI (0.13 g, 0.03 mmol) and CuBr (94 mg, 0.66 mmol). After the evacuation followed with backfilling of nitrogen, anisole (1 mL), distilled MMA (0.63 mL, 6.0 mmol) and N,N,N’,N”,N”-pentamethyldiethylenetriamine (PMDETA) (127 μL, 0.62 mmol) were added. Then the reaction mixture was stirred for 5 min. After five freeze-pump-thaw cycles, the flask was placed in a 100˚C oil bath for 24 h. After dilution with THF, the reaction mixture was filtered with alumina column in order to remove the copper catalyst. After concentration, the polymer was obtained by precipitation from methanol (1.70 g). Judging from GPC trace and ¹H-NMR spectrum, no homopolymer was contained in the product.

Chloroform (analytical grade) was used as a volatile solvent for a solvent evaporation method. Poly (vinyl alcohol) (PVA) (Kuraray, PVA224) as a stabilizer was used as received.

A polymer solution (in chloroform, 2.5% or 5%) was dispersed in ten times volume of water containing 0.3% of PVA with a homogenizer (X520, CAT Scientific, US) to obtain 2 - 10 μm sized droplets (usually 5 min treatment).The weight ratio for the binary blend was fixed to be 1/1 (PBTPA/PMMA). In the case of ternary blends, the content of block copolymer was 10, 30 or 50 wt% keeping the weight ratio of PBTPA component to PMMA component constant (1/1). The homogenized mixture was stirred by a mechanical stirrer at 100 rpm for 24 hr to evaporated CHCl₃ slowly. The resulting microspheres were washed with distilled water four times with a centrifugation process. Finally, polymer seeds dried under vacuum.

Resulting PBTPA and PBTPA-b-PMMA were characterized with ¹H-NMR (ECX 300, JEOL, Japan) and GPC [18] . The surface feature and inside morphologies of microspheres were characterized by scanning electron microscope (SEM) (JSM-6510, JEOL, Japan) and transmission electron microscope (TEM) (JEM-2100, JEOL, Japan), respectively. The specimens for SEM and TEM observations were prepared as described elsewhere [24] . The PBTPA domain was stained by exposing the specimens to the vapor of an aqueous RuO₄ solution (0.5%) for 90 min in a sealed bottle at room temperature.

Figure 1 shows SEM images of microspheres with PBTPA homopolymer fabricated at the initial polymer concentration of 5%. As shown in Figure 1(a), low molecular weight polymer (PBTPA-L) afforded spherical polymer particles with external smooth surface. In the case of high molecular weight polymer (PBTPA-H), Irregular and in some extents, non-spherical larger particles with rough surfaces were produced even at the same experimental conditions (Figure 1(b)). Since the both polymers exhibit the same solubility (miscible in chloroform), it is considered that slightly increased viscosity of the solution made resulting particle irregular and larger in the case of PBTPA-H.

In next step, microspheres based on the binary blend PBTPA/PMMA (weight ratio 1/1) were fabricated, and the effect of molecular weight of PBTPA was investigated. Figure 2 shows microscopic images for the resulting particles (a, c) and dispersed polymer solutions (b, d). Basically bi-compartmental morphologies were observed for both composites. In the case of PSt/PMMA blend (weight ratio 1/1) particles, core-shell morphology is observed when a PVA solution is used as a continuous phase [21] [24] .

As Ge et al. discussed thermodynamically [25] , the interfacial tension between dichloromethane solution of PSt and water at the point of the phase separation should be larger compared with the sum of that between two polymer solutions and that between PMMA solution and water for the core-shell morphology (PMMA; shell, and PSt; core). In this study, it is reasonable that the interfacial tension between chloroform solution of PBTPA and water decreased compared with PSt due to the presence of nitrogen atoms, and is comparable to that between chloroform solution of PMMA and water. PBTPA-L/PMMA composites afforded a Janus like morphology, whereas PBTPA-H/PMMA a dumbbell-like morphology. This difference is probably due to the molecular weight dependence of the interfacial tension between both polymer solutions [25] [26] . Figure 2(b) and Figure 2(d) show the optical micrographs for the dispersions just after the dispersing processes. Those images indicate that phase separation of both PBTPA and PMMA solutions occurs at an early stage in the solvent evaporation process, and the morphology at phase separation retains in final particles. It is noteworthy that the binary blend based on PBTPA-H provided particles with a regular shape and surface smooth morphology compared with PBTPA-H homopolymer.

In order to investigate the effect of block copolymer on the surface and inside morphologies, various amount of PBTPA-b-PMMA was added to the binary blend. All ternary blend particles were fabricated keeping the weight ratio of PBTPA component to PMMA component constant (1/1), and low molecular weight PBTPA-L was utilized. Figure 3 shows SEM images for the particles based on ternary blends. The effect of the ratio of the block copolymer [(a), (b): 10%; (c), (d): 30%; (e), (f); 50%], and the initial concentration dependence on the morphology [(a), (c), (d): 5%; (b), (d), (f): 2.5%] were also investigated. By adding of block copolymer, bi-com- partmental microspheres observed in the binary blends particles were not formed. Ternary blends with 10% of the block copolymers at the initial concentration of 5% afforded particles with some patches on the surface. In the high concentration regions, it is possible that microdomain type, a nonequilibrium morphology is observed, because of high viscosity in the droplets [21] . Particles were fabricated at low initial concentration to assure the equilibrium in the formation of particles. However, as shown in Figure 3(b), more irregular shape was observed at 2.5%. At 5% of total polymer concentration, the increase of the ratio of the block copolymer made the surface smoother as shown in Figure 3(c) and Figure 3(e). At 30%, particles seem to have navel. At 50%, smooth and spherical particles were obtained. At both block copolymer contents, the low initial concentration afforded particles with irregular shapes as shown in Figure 3(d) and Figure 3(f).

In order to investigate morphologies inside microspheres and to explore the origin of unique surface features, TEM measurements were carried out. Figure 4 shows TEM images of microspheres based on ternary blends fabricated from 5% of polymer solutions. At 10% of the block copolymer content, the Janus type morphology was no longer observed, and PMMA-rich bright domain was partially engulfed by PBTPA-rich dark domain as shown in Figure 4(a). It is considered that protruded PMMA rich domain formed patch like morphologies at the surface. At 30%, PMMA-rich domain was almost completely engulfed as shown in Figure 4(b). The formation of navels is attributed to the contact point of two domains near the surface. At 50%, a nearly concentric circle image (Figure 4(c)) exhibits the formation of particles with core-shell morphology. It is generally accepted that the block copolymer plays a role of a compatibilizer and the addition of block copolymer decrease the difference of the interfacial tension between two polymer solutions and solids [27] . Therefore it is expected that size of phase separated domain is decreased. In this experiment, however, the formation of microdomains was not observed, and the type of morphology changed by the addition of block copolymers. In our previous study for the blend of PSt and PMMA, the morphologies changes from core-shell to Janus by the addition of the corresponding block copolymers. Until now it is difficult to explain the discrepancy, and the further study is necessary.