Miktoarm Star Copolymers Prepared by Transformation from Enhanced Spin Capturing Polymerization to Nitroxide-Mediated Polymerization (ESCP-Ŧ-NMP) toward Nanomaterials

Reversible-deactivation radical polymerization (RDRP) serves as a powerful tool nowadays for the preparations of unique linear and non-linear macromolecules. In this study, enhanced spin capturing polymerizations (ESCPs) of styrene (St) and tert-butyl acrylate (tBA) monomers were, respectively, conducted in the presence of difunctional (1Z,1′Z)-1,1′-(1,4-phenylene) bis (N-tert-butylmethanimine oxide) (PBBN) nitrone. Four-arm (PSt)4 and (PtBA)4 star macroinitiators (MIs) can be afforded. By correspondingly switching the second monomer (i.e., tBA and St), miktoarm star copolymers (μ-stars) of (PSt)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2) were thus obtained. We further conducted hydrolysis of the PtBA segments to PAA (i.e., poly(acrylic acid)) in μ-stars to afford amphiphilic μ-stars of (PSt)2-μ-(PAA-b-PSt)2 and (PAA)2-μ-(PSt-b-PAA)2. We investigated each polymerization step and characterized the obtained two sets of “sequence-isomeric” μ-stars by FT-IR, 1H NMR, differential scanning calorimeter (DSC), and thermogravimetric analysis (TGA). Interestingly, we identified their physical property differences in the case of amphiphilic μ-stars by water contact angle (WCA) and atomic force microscopy (AFM) measurements. We thus proposed two microstructures caused by the difference of polymer chain sequences. Through this polymerization transformation (Ŧ) approach (i.e., ESCP-Ŧ-NMP), we demonstrated an interesting and facile strategy for the preparations of μ-stars with adjustable/switchable interior and exterior polymer structures toward the preparations of various nanomaterials.

only slight increases in PDIs), the subsequent chain extensions of NMPs were carried out in a controlled/living radical polymerization fashion. "Sequentially isomeric" μ-stars of (PSt)2-μ-(PtBA-b-PSt) 2 and (PtBA)2-μ-(PSt-b-PtBA)2 were thus afforded. By further hydrolysis of the PtBA segments, another set of sequentially isomeric μ-stars of (PSt)2-μ-(PAA-b-PSt) 2 and (PAA)2-μ-(PSt-b-PAA)2 can be attained. In DSC and TGA analyses, the two sets of sequentially isomeric μ-stars performed similar thermal properties. In WCA measurements of spin-coated μ-star films on wafers, we observed a similar hydrophobicity in (PSt)2-μ-(PtBA-b-PSt) 2 and (PtBA)2-μ-(PSt-b-PtBA)2. Interestingly, we observed quite different wetting behaviors after hydrolysis, indicating a significant contribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated thin films of the amphiphilic μ-stars were further examined by AFM and revealed different morphologies. We thus proposed two microstructures: (i) In the case of (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains. (ii) In the case of (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuous phase mostly covered by a continuous phase of the PAA segments. In sum, the facile polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fascinating strategy for the preparations of μ-stars with switchable/adjustable interior and exterior polymer structures. We eventually acquired amphiphilic μ-stars and demonstrated their significant differences in thin film self-assembly.
only slight increases in PDIs), the subsequent chain extensions of NMPs were carried out in a controlled/living radical polymerization fashion. "Sequentially isomeric" μ-stars of (PSt)2-μ-(PtBA-b-PSt) 2 and (PtBA)2-μ-(PSt-b-PtBA)2 were thus afforded. By further hydrolysis of the PtBA segments, another set of sequentially isomeric μ-stars of (PSt)2-μ-(PAA-b-PSt) 2 and (PAA)2-μ-(PSt-b-PAA)2 can be attained. In DSC and TGA analyses, the two sets of sequentially isomeric μ-stars performed similar thermal properties. In WCA measurements of spin-coated μ-star films on wafers, we observed a similar hydrophobicity in (PSt)2-μ-(PtBA-b-PSt) 2 and (PtBA)2-μ-(PSt-b-PtBA)2. Interestingly, we observed quite different wetting behaviors after hydrolysis, indicating a significant contribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated thin films of the amphiphilic μ-stars were further examined by AFM and revealed different morphologies. We thus proposed two microstructures: (i) In the case of (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains. (ii) In the case of (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuous phase mostly covered by a continuous phase of the PAA segments. In sum, the facile polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fascinating strategy for the preparations of μ-stars with switchable/adjustable interior and exterior polymer structures. We eventually acquired amphiphilic μ-stars and demonstrated their significant differences in thin film self-assembly.
Among RDRP techniques, NMP is recognized as one of the most adaptable techniques for industrial applications due to its simple reaction condition. Previously, the Jérôme group [31,32] and the Barner-Kowollik group [33,34] demonstrated an innovative method called "enhanced spin capturing polymerization" (ESCP), which was basically extended from NMP and can also be broadly classified in the same family. The newly developed ESCP is conducted in conventional free radical polymerization (FRP) conditions but is necessary for adding nitrone compound. During polymerization, intermediates can be effectively formed via a cross-trapping reaction between propagating macroradicals and nitrones. Then one intermediate macroradical can quickly undergo cross-coupling with another propagating macroradical. Accordingly, a new alkoxyamine moiety can result, which can further conduct NMP from the middle of polymer chains. Namely, the transformation from ESCP to NMP (i.e., ESCP-11, x FOR PEER REVIEW 12 of 14 only slight increases in PDIs), the subsequent chain extensions of NMPs were carried out in a controlled/living radical polymerization fashion. "Sequentially isomeric" μ-stars of (PSt)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2 were thus afforded. By further hydrolysis of the PtBA segments, another set of sequentially isomeric μ-stars of (PSt)2-μ-(PAA-b-PSt)2 and (PAA)2-μ-(PSt-b-PAA)2 can be attained. In DSC and TGA analyses, the two sets of sequentially isomeric μ-stars performed similar thermal properties. In WCA measurements of spin-coated μ-star films on wafers, we observed a similar hydrophobicity in (PSt)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2. Interestingly, we observed quite different wetting behaviors after hydrolysis, indicating a significant contribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated thin films of the amphiphilic μ-stars were further examined by AFM and revealed different morphologies. We thus proposed two microstructures: (i) In the case of (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains. (ii) In the case of (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuous phase mostly covered by a continuous phase of the PAA segments. In sum, the facile polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fascinating strategy for the preparations of μ-stars with switchable/adjustable interior and exterior polymer structures. We eventually acquired amphiphilic μ-stars and demonstrated their significant differences in thin film self-assembly.
Combining with RDRPs and several other living polymerization techniques [35][36][37][38][39], sequential polymerization approaches via single chemistry or polymerization transformation (   IEW  12 of 14 ly slight increases in PDIs), the subsequent chain extensions of NMPs were carried out a controlled/living radical polymerization fashion. "Sequentially isomeric" μ-stars of St)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2 were thus afforded. By further hyolysis of the PtBA segments, another set of sequentially isomeric μ-stars of St)2-μ-(PAA-b-PSt)2 and (PAA)2-μ-(PSt-b-PAA)2 can be attained. In DSC and TGA alyses, the two sets of sequentially isomeric μ-stars performed similar thermal propers. In WCA measurements of spin-coated μ-star films on wafers, we observed a similar drophobicity in (PSt)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2. Interestingly, we served quite different wetting behaviors after hydrolysis, indicating a significant conbution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated thin ms of the amphiphilic μ-stars were further examined by AFM and revealed different orphologies. We thus proposed two microstructures: (i) In the case of the interior PAA segments served as a discontinuous phase and ere surrounded by a continuous phase of PSt-rich domains. (ii) In the case of AA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuous ase mostly covered by a continuous phase of the PAA segments. In sum, the facile lymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fasciting strategy for the preparations of μ-stars with switchable/adjustable interior and exteripolymer structures. We eventually acquired amphiphilic μ-stars and demonstrated their nificant differences in thin film self-assembly. ) and (B) 1 H NMR (400 MHz, CDCl3, *: solvent peaks) spectra of PBBN nitrone, Figure S2: FT-IR ectra of μ-stars before and after hydrolysis. ) provided a diverse way to create novel and unique macromolecules [40][41][42], including typical BCPs, soft-hard segmented BCPs, star block copolymers (sBCPs), and miktoarm star copolymers (µ-stars). The polymer chain topology of BCPs typically belongs to the analog of linear type copolymers and comprises at least two chemically linked (im)miscible polymer segments. Accordingly, BCPs can spontaneously conduct interesting microphase separation behaviors to fabricate nanomaterials. By further going to non-linear type "segmented" copolymers, the design of fascinating polymer architectures, such as (A-b-B) n sBCPs and A 2 B/ABC/A 3 B/ABCD µ-stars, has received significant attention due to their specific and unique physical properties [43][44][45][46][47][48]. Several examples studied the effectiveness of sBCPs on the self-assembly behaviors and further addressed the critical effect of "entropy penalty" coming from the nature of complex polymer architectures [49,50].
In an attempt to design unique and specific non-linear copolymers, we herein combine a sequential polymerization transformation of ESCP- Interestingly, observed quite different wetting behaviors after hydrolysis, indicating a significant c tribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated t films of the amphiphilic μ-stars were further examined by AFM and revealed differ morphologies. We thus proposed two microstructures: (i) In the case (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous phase a were surrounded by a continuous phase of PSt-rich domains. (ii) In the case (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuo phase mostly covered by a continuous phase of the PAA segments. In sum, the fa polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fa nating strategy for the preparations of μ-stars with switchable/adjustable interior and ext or polymer structures. We eventually acquired amphiphilic μ-stars and demonstrated th significant differences in thin film self-assembly.

Supplementary Materials:
The following are available online at www.mdpi.com/xxx/s1, Sche S1: Synthesis of (1Z,1′Z)-1,1′-(1,4-phenylene)-bis(N-tert-butylmethanimine oxide) nitrone ( PBBN) (where, t-BuHAA: N-(tert-butyl)hydroxylamine acetate), Figure S1: (A) FT-IR (4000cm −1 ) and (B) 1 H NMR (400 MHz, CDCl3, *: solvent peaks) spectra of PBBN nitrone, Figure S2: FT spectra of μ-stars before and after hydrolysis.  -NMP. As shown in route I in Scheme 1, azobisisobutyronitrile (AIBN) can be thermally activated to generate radicals following the addition of styrene (St) monomer. The single addition of a primary monomer radical can further undergo chain propagations. During polymerizations, the propagating PSt• species can be captured by the difunctional PBBN nitrone in a four-fold molar ratio. Due to the ESCP mechanism being based on a methodology of convergent approach, a four-arm (PSt n ) 4 star homopolymer (homo-star) can be accordingly attained. With tert-butyl acrylate (tBA) as a monomer, as shown in route II in Scheme 1, a four-arm (PtBA x ) 4 star homopolymer (homo-star) can also be attained via the ESCP mechanism. It is more important and interesting that the resulting homo-stars both possess two thermally reversible alkoxyamine moieties that can be subsequently extended to proceed with nitroxide-mediated radical polymerization (NMP). With different polymerization sequences of St and tBA, namely, "sequence-isomers" of miktoarm star copolymers can be facilely obtained that might have different physical properties. We characterized the copolymers using Fourier-transform infrared (FT-IR) spectroscopy, differential scanning calorimetry (DSC), thermogravimetric analysis (TGA), water contact angle (WCA) measurements, and atomic force microscope (AFM). erials 2021, 11, x FOR PEER REVIEW 3 of 14 copolymers using Fourier-transform infrared (FT-IR) spectroscopy, differential scanning calorimetry (DSC), thermogravimetric analysis (TGA), water contact angle (WCA) measurements, and atomic force microscope (AFM).

Characterization
The monomer conversions were analyzed by a Hewlett-Packard gas chromatograph (GC) set (a HP 5890 ser. II FID detector and a CD-5 column). Gel permeation chromatography (GPC) with two PSS SDV columns (linear S and 100 Å) and an RI detector at 35 °C (eluent: tetrahydrofuran (THF); flow rate: 1 mL/min) were used. Characterization of number and weight average molecular weights (i.e., Mn and Mw) and polydispersity (PDI = Mw/Mn) was calculated from a polystyrene calibration line. Functional groups of samples were analyzed with the FT-IR instrument of PerkinElmer Spectrum One. Each sample was drop-casted on a KBr disk and dried in a vacuum for a few hours. A Bruker 400 NMR spectrometer was utilized to record 1 H NMR spectra using CDCl3 (chemical shift (δ) = 7.26 ppm) for calibration. Seiko 6220 differential scanning calorimeter (DSC) was utilized to detect the glass transition temperatures (Tg) of the (co)polymers under N2 (first run up to 180 °C to remove thermal history and quenching; the second run was ramped with 20 °C/min from −10 to 190 °C). TA Instruments Q50 thermogravimetric analysis (TGA) was used to trace the thermal stability of (co)polymers loaded on a platinum holder (runs were ramped with 20 °C/min in the range of 25-700 °C under N2(g)). Water contact angles (WCAs) were measured with the KRÜSS G10 instrument with a neutral DI water droplet (ca. 5 μL). Seiko SPA400 atomic force microscopy (AFM) was used (1 wt% of polymer solutions in 1-methoxy-2-propyl acetate (MPA) were drop-casted onto wafers).

Characterization
The monomer conversions were analyzed by a Hewlett-Packard gas chromatograph (GC) set (a HP 5890 ser. II FID detector and a CD-5 column). Gel permeation chromatography (GPC) with two PSS SDV columns (linear S and 100 Å) and an RI detector at 35 • C (eluent: tetrahydrofuran (THF); flow rate: 1 mL/min) were used. Characterization of number and weight average molecular weights (i.e., M n and M w ) and polydispersity (PDI = M w /M n ) was calculated from a polystyrene calibration line. Functional groups of samples were analyzed with the FT-IR instrument of PerkinElmer Spectrum One. Each sample was drop-casted on a KBr disk and dried in a vacuum for a few hours. A Bruker 400 NMR spectrometer was utilized to record 1 H NMR spectra using CDCl 3 (chemical shift (δ) = 7.26 ppm) for calibration. Seiko 6220 differential scanning calorimeter (DSC) was utilized to detect the glass transition temperatures (T g ) of the (co)polymers under N 2 (first run up to 180 • C to remove thermal history and quenching; the second run was ramped with 20 • C/min from −10 to 190 • C). TA Instruments Q50 thermogravimetric analysis (TGA) was used to trace the thermal stability of (co)polymers loaded on a platinum holder (runs were ramped with 20 • C/min in the range of 25-700 • C under N 2(g) ). Water contact angles (WCAs) were measured with the KRÜSS G10 instrument with a neutral DI water droplet (ca. 5 µL). Seiko SPA400 atomic force microscopy (AFM) was used (1 wt% of polymer solutions in 1-methoxy-2-propyl acetate (MPA) were drop-casted onto wafers).   Figure S1.

ESCPs of St and tBA and Thermolysis of the (PSt) 4 Homo-Star
For the ESCP of St (i.e., route I in Scheme 1), PBBN (36.2 mg, 0.131 mmol), St (6.05 mL, 52.1 mmol), AIBN (21.5 mg, 0.131 mmol), and a few drops of anisole were mixed in a Schlenk flask. The reaction flask was sealed and degassed through four freeze/pump/thaw cycles. The flask was placed in an oil bath at 80 • C and the monomer conversion was traced by GC. The molecular weight of the product was estimated by using GPC. To stop the reaction, the flask was cooled by an ice bath and exposed to air. The solution was diluted with THF and precipitation in MeOH. The powder was collected and dried in a vacuum oven to remove residual solvent. White powder of 4-arm PSt homopolymer (i.e., (PSt) 4 homo-star: yield 36.5%, M n = 17760, PDI = 1.53) was used. For the ESCP of tBA (i.e., route II in Scheme 1), the procedures were similar to route I and afforded pale yellow viscous liquid of 4-arm PtBA homopolymer (i.e., (PtBA) 4 homo-star: yield 32.5%, M n = 13560, PDI = 1.55).

Synthesis of Miktoarm Star (µ-Star) Copolymers via Nitroxide-Mediated Chain Extensions of Homo-Stars and Hydrolysis of PtBA Segments
For the nitroxide-mediated chain extensions of homo-stars (i.e., route III(i) in Scheme 2), (PSt) 4 homo-star (0.82 g, 0.03 mmol) macroinitiator, tBA (0.351 mL, 2.42 mmol), and anisole were added to a Schlenk flask. The degassing method was similar to the above-mentioned procedures for removing oxygen. The flask was placed in a 125 • C oil bath and the monomer conversion was traced by GC. The molecular weight evolution was monitored by GPC. After a desired period, the reaction was quenched and opened to air. The mixture was diluted with DCM and precipitated in MeOH: H 2 O = 8/2 (v/v). Yellowish white powder of (PSt) 2 -µ-(PtBA-b-PSt) 2 miktoarm star (µ-star) copolymer was acquired (yield 71%). With (PtBA) 4 homo-star as a macroinitiator and St as a monomer (i.e., route IV(i) in Scheme 2); similarily, yellowish-white powder of (PtBA) 2 -µ-(PSt-b-PtBA) 2 µ-star copolymer was acquired (yield 54.9%).
An example of hydrolysis: (PtBA) 2 -µ-(PSt-b-PtBA) 2 µ-star (0.721 g, 60.1 µmol), trifluoroacetic acid (0.502 mL, 6.11 mmol), and DCM (15.1 mL) were mixed and kept overnight at room temperature. After the reaction was completed, the mixture was purified by dialysis membrane (MWCO = 3500) for three days using DMSO: DI water = 5/95 (v/v). The purified solution was freeze-dried to remove water. White powder of (PAA) 2 -µ-(PSt-b-PAA) 2 µ-star was obtained (yield 57.8%). To obtain (PSt) 2 -µ-(PAA-b-PSt) 2 , similar procedures were conducted. FT-IR spectra of the obtained µ-star copolymers before and after hydrolysis are shown in Figure S2. In Figure 1a, both cases of ESCPs (i.e., solid symbols) showed deviations in a short reaction time. In Figure 1b,c, we obtained broad molecular weight distributions (i.e., PDI > 1.5) and only slight changes in molecular weights (MWs) concerning the monomer conversions (i.e., M n,PSt = ca. 16k and M n,PtBA = ca. 13k). As shown in the corresponding GPC traces in Figure 2, broad mono-modal curves can be observed with only slight changes in MWs. These results indicate that the polymerizations were poorly controlled and that high PDI values were obtained. Based on the reported mechanism, an ESCP typically proceeds in a conventional free radical polymerization fashion. Namely, ESCP possesses the non-RDRP feature. These results are similar to the reported studies [33,34]. As illustrated in Scheme 1, two macroinitiators of 4-arm (PSt) 4 and (PtBA) 4 star homopolymers (homo-stars) were thus obtained, which both possess two active arms connected by the alkoxyamine moieties to the star center. Namely, thermal dissociability of the macroinitiators can be expected. Figure 1a, both cases of ESCPs (i.e., solid symbols) showed deviations in a short reaction time. In Figure 1b,c, we obtained broad molecular weight distributions (i.e., PDI > 1.5) and only slight changes in molecular weights (MWs) concerning the monomer conversions (i.e., Mn,PSt = ca. 16k and Mn,PtBA = ca. 13k). As shown in the corresponding GPC traces in Figure 2, broad mono-modal curves can be observed with only slight changes in MWs. These results indicate that the polymerizations were poorly controlled and that high PDI values were obtained. Based on the reported mechanism, an ESCP typically proceeds in a conventional free radical polymerization fashion. Namely, ESCP possesses the non-RDRP feature. These results are similar to the reported studies [33,34]. As illustrated in Scheme 1, two macroinitiators of 4-arm (PSt)4 and (PtBA)4 star homopolymers (homo-stars) were thus obtained, which both possess two active arms connected by the alkoxyamine moieties to the star center. Namely, thermal dissociability of the macroinitiators can be expected.   Figure 3A, the NO-PSt linkages can be thermally dissociated and generated two types of PSt macroradicals. In the presence of excess amounts of TBTH reducing agent, mixed PSt chains can be thus obtained, which are composed of linked two arms (i.e., one single (PSt)2 chain) and two single arms (i.e., two PSt chains). After the   Figure 1b,c, we obtained broad molecular weight distributions (i.e., PDI > 1.5) and only slight changes in molecular weights (MWs) concerning the monomer conversions (i.e., Mn,PSt = ca. 16k and Mn,PtBA = ca. 13k). As shown in the corresponding GPC traces in Figure 2, broad mono-modal curves can be observed with only slight changes in MWs. These results indicate that the polymerizations were poorly controlled and that high PDI values were obtained. Based on the reported mechanism, an ESCP typically proceeds in a conventional free radical polymerization fashion. Namely, ESCP possesses the non-RDRP feature. These results are similar to the reported studies [33,34]. As illustrated in Scheme 1, two macroinitiators of 4-arm (PSt)4 and (PtBA)4 star homopolymers (homo-stars) were thus obtained, which both possess two active arms connected by the alkoxyamine moieties to the star center. Namely, thermal dissociability of the macroinitiators can be expected.   Figure 3A, the NO-PSt linkages can be thermally dissociated and generated two types of PSt macroradicals. In the presence of excess amounts of TBTH reducing agent, mixed PSt chains can be thus obtained, which are composed of linked two arms (i.e., one single (PSt)2 chain) and two single arms (i.e., two PSt chains). After the  Figure 3A, the NO-PSt linkages can be thermally dissociated and generated two types of PSt macroradicals. In the presence of excess amounts of TBTH reducing agent, mixed PSt chains can be thus obtained, which are composed of linked two arms (i.e., one single (PSt) 2 chain) and two single arms (i.e., two PSt chains). After the thermolysis reaction, as shown in Figure 3B, MWs displayed a negative evolution in GPC traces from curve b (i.e., the original (PSt) 4 : M n = 16,120 and PDI = 1.52) to curve a (M n,overall = 8900 and PDI = 1.34). The significant decrease in MW was reasonably ascribed to the cleavage of (PSt) 4 homo-star, reductions of PSt macroradicals, and generations of single indivisible (PSt) 2 (i.e., species 1) and two cleaved PSt chains (i.e., species 2). At the end of curve b in Figure 3B, an elevated trend might be due to the baseline deviation issue. These results rationally revealed the presence of reversible alkoxyamine moiety in the homo-stars that can be further carried out post-polymerizations. traces from curve b (i.e., the original (PSt)4: Mn = 16120 and PDI = 1.52) to curve a (Mn,overall = 8900 and PDI = 1.34). The significant decrease in MW was reasonably ascribed to the cleavage of (PSt)4 homo-star, reductions of PSt macroradicals, and generations of single indivisible (PSt)2 (i.e., species 1) and two cleaved PSt chains (i.e., species 2). At the end of curve b in Figure 3B, an elevated trend might be due to the baseline deviation issue. These results rationally revealed the presence of reversible alkoxyamine moiety in the homo-stars that can be further carried out post-polymerizations. As shown in routes III(i) and IV(i) in Scheme 2, we can expect that the two dissociable NO-PSt linkages can be thermally reactivated and proceed with NMP of second monomer to afford miktoarm star (μ-star) copolymers. With different polymerization sequence sets, we can conduct chain extensions of (PSt)4 and (PtBA)4 homo-star macroinitiators (MIs) with a different second monomer in bulk (i.e., tBA and St, respectively). Figure 4 displays kinetic plots of the chain extensions of (PSt)4 with tBA (i.e., circle symbols) and (PtBA)4 with St (i.e., square symbols). As shown in Figure 4a, both chain extension cases performed a gradual consumption of monomers. Linear first-order reactions were observed in each case. An apparent faster consumption in the chain extension with tBA (kapp(tBA) = (7.34 ± 0.6) × 10 −4 s −1 ) and a slower reaction rate in the chain extension with St (kapp(St) = (1.18 ± 0.2) × 10 −4 s −1 ) were acquired. The significant difference (kapp(tBA)/kapp(St) = ca. 6 times) might be ascribed to obvious difference of propagation rate constants of the two monomers (e.g., kp(tBA) = ca. 10 4 s −1 and kp(St) = ca. 10 3 s −1 at 125 °C) [7,51]. As shown in Figure 4b, PDI values of less than 1.7 were acquired in the conversion of less than 70%. With the conversion of ca. 90%, a high PDI value (= ca. 2.11) was observed that might be due to the occurrence of side reactions. Several side reactions during NMPs were reported, mainly including disproportionation of the dissociated alkoxyamines, cross-reactions of intramolecular/intermolecular hydrogen-transfer, and irreversible N-OC bond cleavage [5,52]. As shown in Figure 4c, however, we observed an unexpected slight decrease trend in MWs. It is reported that the more complex molecular architectures cause smaller hydrodynamic volumes in the same solution environment in As shown in routes III(i) and IV(i) in Scheme 2, we can expect that the two dissociable NO-PSt linkages can be thermally reactivated and proceed with NMP of second monomer to afford miktoarm star (µ-star) copolymers. With different polymerization sequence sets, we can conduct chain extensions of (PSt) 4 and (PtBA) 4 homo-star macroinitiators (MIs) with a different second monomer in bulk (i.e., tBA and St, respectively). Figure 4 displays kinetic plots of the chain extensions of (PSt) 4 with tBA (i.e., circle symbols) and (PtBA) 4 with St (i.e., square symbols). As shown in Figure 4a, both chain extension cases performed a gradual consumption of monomers. Linear first-order reactions were observed in each case. An apparent faster consumption in the chain extension with tBA (k app(tBA) = (7.34 ± 0.6) × 10 −4 s −1 ) and a slower reaction rate in the chain extension with St (k app(St) = (1.18 ± 0.2) × 10 −4 s −1 ) were acquired. The significant difference (k app(tBA) /k app(St) = ca. 6 times) might be ascribed to obvious difference of propagation rate constants of the two monomers (e.g., k p(tBA) = ca. 10 4 s −1 and k p(St) = ca. 10 3 s −1 at 125 • C) [7,51]. As shown in Figure 4b, PDI values of less than 1.7 were acquired in the conversion of less than 70%. With the conversion of ca. 90%, a high PDI value (= ca. 2.11) was observed that might be due to the occurrence of side reactions. Several side reactions during NMPs were reported, mainly including disproportionation of the dissociated alkoxyamines, cross-reactions of intramolecular/intermolecular hydrogen-transfer, and irreversible N-OC bond cleavage [5,52]. As shown in Figure 4c, however, we observed an unexpected slight decrease trend in MWs. It is reported that the more complex molecular architectures cause smaller hydrodynamic volumes in the same solution environment in comparison to those of linear polymers in a similar MW [20,53]. In the GPC analysis, we utilized linear PSt as the calibration standard. Another possible reason is that the insertion of polymer chains during NMP led to the formation of µ-star copolymers with an asymmetric molecular conformation. Thus, the MW deviations could be rationally ascribed to the synergistic effects of asymmetry and star-shaped architecture. As shown in Figure 5, the corresponding GPC traces displayed a monomodal and only slight increases in PDI values in moderate conversions. These results thus indicated the subsequent chain extensions of NMPs, proceeding in a controlled/living radical polymerization fashion. Accordingly, the unique and facile multisite polymerization transformation ( ESCP to NMP (i.e., ESCP-observed quite different wetting behaviors after hydrolysis, indicating a significant contribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coated thin films of the amphiphilic μ-stars were further examined by AFM and revealed different morphologies. We thus proposed two microstructures: (i) In the case of (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains. (ii) In the case of (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discontinuous phase mostly covered by a continuous phase of the PAA segments. In sum, the facile polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting and fascinating strategy for the preparations of μ-stars with switchable/adjustable interior and exterior polymer structures. We eventually acquired amphiphilic μ-stars and demonstrated their significant differences in thin film self-assembly.
The thermal stability of the µ-star copolymers and relevant homopolymers was examined by TGA and displayed in Figure 8. Linear PSt, PtBA, and PAA were shown in traces a-c. In the cases of (PSt) 2 -µ-(PtBA-b-PSt) 2 and (PtBA) 2 -µ-(PSt-b-PtBA) 2 µ-star copolymers (i.e., curves d and e with solid symbols), similar two-step decomposition profiles were observed. Two maximum rates (r d ) were revealed at approximately 250 and 410 • C, respectively. The first step might be mainly due to pyrolysis of the pendent tBu bulky group of PtBA segments. Then the second step arose from pyrolysis of the residual main chains. The thermal stabilities, based on 5 wt% weight loss temperatures (T d5% ), were similar at approximately 232 • C. The char yields were both approximately 0.5 wt%. In the cases of (PSt) 2 -µ-(PAA-b-PSt) 2 and (PAA) 2 -µ-(PSt-b-PAA) 2 µ-star copolymers (i.e., curves f and g with hollow symbols), two-step decomposition profiles were also observed. However, the first step showed a gradual decomposition profile in both cases. It is rationally due to Nanomaterials 2021, 11, 2392 9 of 14 continuous dehydration and pyrolysis of the pendent carboxylic acid of PAA segments. Then the second step also arose from pyrolysis of the residual main chains. T d5% s were about 220 and 165 • C, respectively. Char yields were both approximately 0.3 wt%. vealed its stable hydrophobicity. With the nature of immiscible PSt and PAA chains, we deduced that a low wettability microstructure having PAA segments as a discontinuous phase surrounded by a continuous phase of PSt segments as was formed. As displayed in the set of Figure 9d, we initially observed a similar WCA of ca. 90.9 ± 4.7° in the (PAA)2-μ-(PSt-b-PAA)2 sample. With different holding times, interestingly, we then observed a significant decrease of WCAs in a minute to ca. 24.9 ± 2.3°. The WCA changes were due to the surficial swelling behaviors between the PAA segments and water droplets [54]. Accordingly, we deduced that a wettable microstructure with PSt segments as a discontinuous phase covered by a continuous phase of PAA segments was constructed. The significant different hydrophobic properties are synergy via the complex μ-star architecture and amphiphilic polymer chains. 25 50 75 100 125 150 175 Heat Flow ( Endo) Residual Weight (%) The µ-stars were spin-coated on silicon wafers and the hydrophobicity was analyzed through water contact angle (WCA) measurements. As shown in Figure 9a,b, the WCAs of (PSt) 2 -µ-(PtBA-b-PSt) 2 and (PtBA) 2 -µ-(PSt-b-PtBA) 2 were ca. 99.9 ± 4.5 • and 104.6 ± 5.6 • , respectively. The results revealed their similar hydrophobicity despite the different interior and exterior sequences of PSt and PtBA chains. After hydrolysis of the pendent group of PtBA segments, we further examined WCAs vs. different holding times. As displayed in the set of Figure 9c, we initially observed a WCA of ca. 98.9 ± 5.2 • in the (PSt) 2 -µ-(PAA-b-PSt) 2 sample. With different holding times, we then observed a slight decrease of WCAs in a minute to ca. 83.5 ± 4.3 • . The only slight decreases in WCAs revealed its stable hydrophobicity. With the nature of immiscible PSt and PAA chains, we deduced that a low wettability microstructure having PAA segments as a discontinuous phase surrounded by a continuous phase of PSt segments as was formed. As displayed in the set of Figure 9d, we initially observed a similar WCA of ca. 90.9 ± 4.7 • in the (PAA) 2 -µ-(PSt-b-PAA) 2 sample. With different holding times, interestingly, we then observed a significant decrease of WCAs in a minute to ca. 24.9 ± 2.3 • . The WCA changes were due to the surficial swelling behaviors between the PAA segments and water droplets [54]. Accordingly, we deduced that a wettable microstructure with PSt segments as a discontinuous phase covered by a continuous phase of PAA segments was constructed. The significant different hydrophobic properties are synergy via the complex µ-star architecture and amphiphilic polymer chains.  The above two amphiphilic μ-stars were then dissolved in 1-methoxy-2-propyl acetate (MPA) (1 wt%) and drop-casted on silicon wafers to analyze the morphology by AFM. Figure 10  The above two amphiphilic µ-stars were then dissolved in 1-methoxy-2-propyl acetate (MPA) (1 wt%) and drop-casted on silicon wafers to analyze the morphology by AFM. Figure 10 displays the topologies of (PSt) 2 -µ-(PAA-b-PSt) 2 and (PAA) 2 -µ-(PSt-b-PAA) 2 µ-stars that both indicated quite smooth coating films. The height image in Figure 10a revealed a morphology with isolated dark domains surrounded by a continuous white matrix. The corresponding phase image in Figure 10a displayed an opposite color compared to that of the height image. The isolated white domains resulted from hard PAA chains that possess a high T g of ca. 135 • C. Thus, the continuous dark matrix was mainly composed of softer PSt chains (T g = ca. 100 • C). From the abovementioned two images, we thus proposed a microstructure that was inserted in the middle of Figure 10a. The proposed microstructure elucidated that the interior PAA segments (i.e., blue-colored chains) served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains (i.e., black colored chains). In the case with an alternative sequence of (PAA) 2 -µ-(PSt-b-PAA) 2 µ-star, the height image in Figure 10b displayed a connected particle-like morphology. The corresponding phase image in Figure 10b showed major white and light-brown colors, indicating the surface was majorly composed of hard PAA segments. From the two images in Figure 10b, a proposed microstructure was also inserted. The proposed microstructure indicated that the interior PSt segments (i.e., black-colored chains) served as a discontinuous phase mostly covered by a continuous phase of the PAA segments (i.e., blue-colored chains). The two proposed microstructures could also be consistent with the behaviors observed in the WCA measurements. Interestingly, we first demonstrated changeable µ-star chemical structures via polymerization sequence control led to dissimilar physical properties composing different sequenced µ-stars.
played a connected particle-like morphology. The corresponding phase image in Figure  10b showed major white and light-brown colors, indicating the surface was majorly composed of hard PAA segments. From the two images in Figure 10b, a proposed microstructure was also inserted. The proposed microstructure indicated that the interior PSt segments (i.e., black-colored chains) served as a discontinuous phase mostly covered by a continuous phase of the PAA segments (i.e., blue-colored chains). The two proposed microstructures could also be consistent with the behaviors observed in the WCA measurements. Interestingly, we first demonstrated changeable μ-star chemical structures via polymerization sequence control led to dissimilar physical properties composing different sequenced μ-stars.

Conclusions
ESCPs of St and tBA monomers with PBBN as the capturing agent were first demonstrated. We then obtained 4-arm (PSt)4 and (PtBA)4 homo-stars with two thermally reversible alkoxyamine moieties. In the presence of excess amounts of TBTH, the dissociations of NO-C linkages can be revealed by GPC traces. The 4-arm (PSt)4 and (PtBA)4 macroinitiators were subsequently proceeded by NMPs of tBA and St, respectively. We observed first-order kinetic plots but the GPC traces showed unexpected decrease trends in MWs. This might be attributed to the synergistic influences of asymmetry and star-shaped architecture. Combining kinetic data with GPC traces (i.e., a monomodal and

Conclusions
ESCPs of St and tBA monomers with PBBN as the capturing agent were first demonstrated. We then obtained 4-arm (PSt) 4 and (PtBA) 4 homo-stars with two thermally reversible alkoxyamine moieties. In the presence of excess amounts of TBTH, the dissociations of NO-C linkages can be revealed by GPC traces. The 4-arm (PSt) 4 and (PtBA) 4 macroinitiators were subsequently proceeded by NMPs of tBA and St, respectively. We observed first-order kinetic plots but the GPC traces showed unexpected decrease trends in MWs. This might be attributed to the synergistic influences of asymmetry and starshaped architecture. Combining kinetic data with GPC traces (i.e., a monomodal and only slight increases in PDIs), the subsequent chain extensions of NMPs were carried out in a controlled/living radical polymerization fashion. "Sequentially isomeric" µ-stars of (PSt) 2µ-(PtBA-b-PSt) 2 and (PtBA) 2 -µ-(PSt-b-PtBA) 2 were thus afforded. By further hydrolysis of the PtBA segments, another set of sequentially isomeric µ-stars of (PSt) 2 -µ-(PAA-b-PSt) 2 and (PAA) 2 -µ-(PSt-b-PAA) 2 can be attained. In DSC and TGA analyses, the two sets of sequentially isomeric µ-stars performed similar thermal properties. In WCA measurements of spin-coated µ-star films on wafers, we observed a similar hydrophobicity in (PSt) 2 -µ-(PtBAb-PSt) 2 and (PtBA) 2 -µ-(PSt-b-PtBA) 2 . Interestingly, we observed quite different wetting behaviors after hydrolysis, indicating a significant contribution from the polymer chain sequence in amphiphilic µ-stars. The spin-coated thin films of the amphiphilic µ-stars were further examined by AFM and revealed different morphologies. We thus proposed two microstructures: (i) In the case of (PSt) 2 -µ-(PAA-b-PSt) 2 , the interior PAA segments served as a discontinuous phase and were surrounded by a continuous phase of PSt-rich domains. (ii) In the case of (PAA) 2 -µ-(PSt-b-PAA) 2 , oppositely, the interior PSt segments served as a discontinuous phase mostly covered by a continuous phase of the PAA segments. In sum, the facile polymerization transformation strategy of ESCP-analyses, the two sets of sequentially isomeric μ-stars performed similar thermal p ties. In WCA measurements of spin-coated μ-star films on wafers, we observed a hydrophobicity in (PSt)2-μ-(PtBA-b-PSt)2 and (PtBA)2-μ-(PSt-b-PtBA)2. Interesting observed quite different wetting behaviors after hydrolysis, indicating a significa tribution from the polymer chain sequence in amphiphilic μ-stars. The spin-coat films of the amphiphilic μ-stars were further examined by AFM and revealed di morphologies. We thus proposed two microstructures: (i) In the ca (PSt)2-μ-(PAA-b-PSt)2, the interior PAA segments served as a discontinuous pha were surrounded by a continuous phase of PSt-rich domains. (ii) In the c (PAA)2-μ-(PSt-b-PAA)2, oppositely, the interior PSt segments served as a discont phase mostly covered by a continuous phase of the PAA segments. In sum, th polymerization transformation strategy of ESCP-Ŧ -NMP provides an interesting an nating strategy for the preparations of μ-stars with switchable/adjustable interior and or polymer structures. We eventually acquired amphiphilic μ-stars and demonstrate significant differences in thin film self-assembly.

Funding:
The authors acknowledge the financial support from the Ministry of Science an nology (MOST108-2923-E-005-001-MY2 and MOST109-2221-E-005-071) and the Energy F Ministry of Economic Affairs, Taiwan. This research is also funded by the 2-institution Co-R Scholarship provided by Kasetsart University and National Chung Hsing University.

Conflicts of Interest:
The authors declare no conflict of interest.