Polymer-Blends

A polymer blend is a class of materials in which two or more polymers are mixed together to yield new materials possessing different features than the initial polymers. Blending is generally aimed at getting new materials with property profiles superior to the features of the individual components. It is also often considered as a 

Here the different steps of the preparation of the nanocomposites are briefly summarized. First, PPO (a low molar mass polymer powder supplied by Sabic-IP, the Netherlands] was end-capped by acetylation in order to avoid inhibition of the styrene polymerization by phenolic OH groups. It was subsequently mixed with styrene and hexadecane. Then the mixture was added to an aqueous solution of 4-dodecylbenzenesulfonic acid (SDBS). This mixture of SDBS/ hexadecane was chosen as a stabilization system since it is suitable to achieve and guarantee efficient stabilization of polymer particles of sizes smaller than 1 ymP The emulsification process was split up into two steps, namely, a first pre-emulsification step performed by ultra-high shear stirring, followed by ultrasonication in order to obtain submicron particles. Finally, the polymerization was initiated and carried out at 80°C under inert atmosphere (final monomer conversion of 90 %]. The latex obtained had a solid content of 23.6 wt% and contained 10 wt% of PPO dissolved in PS and had a particle size of 100 nm. At the end of the polymerization, the PS molar mass was about 

As already highlighted during the study of the previous CNT/ polymer nanocomposites, the low percolation threshold is certainly favored by the viscosity of the polymer matrix, which is notably lower than that of the PS matrix studied in Section 4.2.2. of chapter 4 of this book [about 5 x lO Pa.s for PPO/PS, which is at least one order of magnitude lower than the viscosity of the earlier described PS matrix, which is higher than 10 Pa.s].  

Glass transition temperature [Tg] values of the same PPO/PS blend, with and without MWCNTs, were measured with DSC. The results of these measurements are collected in Table 5.2. 

PPO/PS without CNTs after freeze drying, before thermal treatment 

Some polymers can be mixed homogeneously with others at a molecular level over a wide range of compositions in such a way that there is only one phase present, but most cannot. Immiscible polymer compositions can, however, often be induced to coexist at a variety of coarser levels of mixing, similar in some instances to the structure of cement, but on a much finer scale. In the next section the factors that determine the mixing behaviour are considered. First it is useful to give some definitions. 

A miscible polymer blend is one for which the miscibihty and homogeneity extend down to the molecular level, so that there is no phase separation. An immiscible blend is one for which phase separation occurs, as described in the next section. An immiscible blend is called compatible if it is a useful blend wherein the inhomogeneity caused by the different phases is on a small enough scale not to be apparent in use. (Blends that are miscible in certain useful ranges of composition and temperature, but immiscible in others, are also sometimes called compatible blends.) Most blends are immiscible and can be made compatible only by a variety of compatibilisation techniques, which are described in section 12.2.4. Such compatibilised blends are sometimes called polymer alloys. 

For a polymer solution of polymer 1 in another polymer 2, the Flory-Huggins free energy is 

Based on the random phase approximation the static structure factor S(k) of the blend is given 

Therefore at each point of the spinodal curve, the scattered intensity [which is proportional to S(fe)] in small-angle scattering diverges. For the symmetric blend, = n2 = n, it follows from 

Equation (139) is used to determine the interaction parameter x by measuring It has 

X can actually be attributed to the contribution of density fluctuations to the free energy of the blend which are ignored in equation (139). 

Polymer blends may be expected to reflect the balance of forces that control their phase structure in the bulk. If two polymers are compatible in the bulk, they may or may not segregate in the surface depending on the balance of forces. Materials that are able to phase separate will segregate in the surface, and generally speaking the lower surface energy material will move towards the free air surface. This effect was illustrated in Chapter 9 in the case of the surface segregation of the ether soft block in the case of block polyurethane copolymers. 

Polymer Blends.—In addition to the work on polyester—polyamide blends reported in Section 2, several other papers describe the characteristics of various polymer formulations with polyamides. Biconstituent fibres have been formed from nylon-6 and poly(ethylene terephthalate). The same polyamide and nylon-12 have been blended with acrylonitrile-butadiene-styrene copolymer and the temperature and the concentration dependence of the dynamic modulus evaluated. The rheological properties of acrylonitrile-styrene copolymer/nylon-6 mixture have also been reported. Fourier transform infrared studies of nylon-6 and PVC have indicated the presence of specific interactions between the two polymers in both the molten and solid states. Finally X-r y studies carried out on injection-moulded blends of nylon-6, -12, and -66, have revealed that the addition of small amounts of the second component initiates formation of the y-crystalline phase within the nylon-6 polymer matrix.  

Nagendra, A. Misra, V. Chowdhury, and D. S. Varma, Angew. Makromol. Chem., 1980,90,57. 

In order to predict polymer-polymer miseibility, we might turn to the Flory-Fluggins theory, where eaeh lattiee site has an interaeting segment volume v. Dividing both sides of Eq. (9.3.20) by the total mixture volume Fand using the definition of the interaetion parameter given by Eq. (9.3.18) yields 

Beeause both Uj and V2 are substantially greater than v, the first two terms on the right-hand side of Eq. (9.6.2) are negfigible compared to the third term. As a consequence, AG = AHj and miscibility depends entirely on the energeties of intermolecular interactions. In other words, a negative value of Ae or, equivalently, of the interaction parameter is needed to assiue polymer-polymer miscibility. 

Example 9.4 If the 1 g of polymer of Example 9.1 is dissolved in 9g of a different polymer of molecular weight 80,000, what would be the entropy change on mixing Assume that the density of the two polymers is the same. 

This number is almost three orders of magnitude smaller than those calculated in Example 9.1. 

There is no general theory that might predict a priori as to which polymer pairs are likely to be miscible with each other. However, if the solubility parameters of two polymers are matched, then any favorable interactions between 

FTIR spectroscopy was used to study the polymerisation of random copolymers of 4-vinylphenol with n-alkyl methacrylates which were prepared by free radical copolymerisation of 4-t-butyldimethyl-silyloxystyrene and the corresponding alkyl methacrylates in benzene at 60 °C using azobisiso-butyronitrile (AIBN) as an initiator (321). The thermal reaction of polyphenylene-1,2-dibromoethylene under argon flow was investigated using in situ kinetic IR spectroscopy (345). 

Stopped-flow FTIR spectroscopy was used to follow group transfer polymerisation (GTP) and cyclic oligomeric carbonate formation. The effect of catalyst structure, propagating end stereochemistry and degree of polymerisation on the rate of monomer addition in GTP was investigated (329). 

Compatible blends are two-phase materials with properties controlled by the properties and geometry of each phase and the nature of the connectivity between phases (compatiblilisers modify/improve the interface). In some cases, the addition of small amoimts of an A/B copolymer compatibiliser will result in a compatibilised A-B blend morphology that has improved mechanical properties. The compatibiliser is considered to be located mainly at the interface between the two immiscible polymers, where it induces local miscibility. The compatibliser lowers the interfacial tension and allows the dispersion of the incompatibile homopolymers into small, microscopic domains. 

PEI resin may also be combined with other polymers. In general, to produce a useful blend, the free energy of mixing AG [Eq. (8.11)] must be favorable. 

PEI forms miscible blends with polyesters such as polybutylene tereph-thalate (PBT), polyethylene terephthalate (PET), and polyethylene naph-thanoate (PEN) [30-32]. These blends have a single Tg between that of the PEI and that of polyester. In blends with slower crystallizing polyesters such as PET and PEN, crystalhzation is reduced and one-phase, transparent compositions can be molded. Such blends have reduced thermal performance versus the base PEI polymer, but improved melt flow, reduced yellowness, and slightly better solvent resistance. 

Phase-separated PEI blends have been investigated. Combinations of PEI with polycarbonate (PC) or polycarbonate ester (PCE) copolymers have a fine, laminar two-phase morphology [36]. Combinations of PEI with polycarbonate or polyester carbonates yield a family of two-phase opaque systems that have reduced heat capability versus PEI, but show improved impact and better melt flow [37, 38]. 

Combinations of PEI resins with polyamides (nylons) also produce phase-separated blends with fine particle morphology and good mechanical properties, hkely arising from phase adhesion between the two resins 

PEI blends have also been further modified with silicone polyether-imide copolymer to improve impact strength, especially at lower temperatures. Use of a sihcone polyetherimide as an impact modifier has the added benefit of retaining or even improving flame retardance, as it has a lower fuel value than traditional rubbery impact modifiers. The sili-cone-PEI copolymer also has the stabihty needed to survive high PEI processing temperatures without decomposition. These PEI-sdicone copolymer blends are hazy or opaque, phase-separated systems. 

Polymer alloys are generally named polymer blends within the polymer community. In a recent overview of such blends, Robeson (1994) points out that the primary reason for the surge of academic and industrial interest in polymer blends is directly related to their potential for meeting end-use requirements . He points out that, in general, miscible polymer pairs confer better properties, mechanical ones in particular, than do phase-separated pairs. For instance, the first commercial 

Some very peculiar features have been discovered in the microstructures of copolymers. Thus, Hanna et al. (1993) showed that a random copolymer of two aromatic monomers has chains in which random but similar sequences of the two monomers on distinct chains find each other and come into register to form a 

The principal methods of mixing two kinds of polymer molecules include mechanical blending, graft copolymerization, block copolymerization, and interpenetration of two networks. The last two are often considered as subgroups of the graft method. 

Nodax can be blended with other biodegradable polymers such as polylactic acid and thermoplastic starch for improved processing performance. 

In the analysis of polymer blends the identification and subsequently the characterization of the distribution of the components of the blend (surface coverage and dispersion) is of prime interest. The already mentioned materials contrast in various AFM modes provides a straightforward differentiation of, e.g. glassy and rubbery phases (after considering the effect of frequency on the corresponding transition temperatures). As different components in a blend tend to possess different surface 

The appropriate use of sample preparation procedures to expose the interior (bulk) of a blend of interest is in many cases required. In addition, selective solvent treatments may assist to unequivocally identify the different phase, as illustrated in Fig. 3.59 [133]. In this example, the polystyrene phase in a blend of polystyrene and poly (n-butyl methacrylate) was identified by selective removal of the PS using cyclohexane. Thus the protrusion seen in the height image in panel (a), which are attributed to PS domains, are no longer detectable in panel (b). 

This effect requires polymer blends with well-defined morphologies and optimum micromechanisms. The preparation and study of the morphology and properties of polymer blends have been one of the major areas of polymer research in the past decades. A number of books and detailed reviews have been published on this subject [1-5] an excellent overview on the micro- and nanostructure of polymer blends is [5j. 

Grafting of PS onto LDPE via y irradiation allows the formation of small PS domains in the LDPE matrix see Fig. 4.4. The smallest PS domains of about 40 nm in micrograph (a) correspond to PS macromolecular coils with molecular weights of about 10 coiled PS macromolecules between PE lamellae are sketched in Fig. 4.4(b). As the degree of grafting increases, the PS domains grow in size see Fig. 4.31 [7]. 

Rgure 4.4 PS/LDPE blends after grafting styrene onto PE with small PS particles (bright) in the LDPE matrix grafting efficiency 10% [7]  

Rgure 4.6 Network morphology of a PS/PE (90/10) blend with smaller PS particles in a PE network (stained, ultrathin section, TEM) [9] 

Both PE types show only a separation between the lamellae with long, thicker lamellae of HOPE and thinner lamellae with internal defect layers of LDPE. 

Applications of the spin-label technique to polymer blends have been relatively recent. Shimada et al. have studied blends of end-labelled poly(ethylene oxide)- 

Figore9 ESR spectrum of 0.1% (w/w) fumarate-vinyl acetate copolymer, 2% dot-riacontane in dodecane (a) 23 °C, above the cloud point (b) 19 °C, just below the cloujd point (c) 15 °C 

Similar results were obtained with a blend of chain-end labelled PMMA (prepared by group transfer polymerisation) and an immiscible partner, poly(2-ethylhexyl methacrylate), of low T, (263 K) [36], 

These observations are in accord with Helfand s general theory that at thermodynamic equilibrium the interphase in a blend of immiscible polymers 

FigareM Extremaseparationvs.temperatureforpurePS, 0 1 1 blend of PS and PIP, 1 39 blend of PS and PIP, A. Reproduced from [11] with permission of Pergamon Press Ltd., Headington HiU Hall, Oxford 0X3 OBW, UK 

Nguyen and co-workers [110, 111] used adsorption/desorption chromatography to physically separate binary component blends of PS with PMMA and PS with polyvinyl acetate (PVAc). This technique was coupled to SEC in order to separate the blend components by size. Full adsorption/desorption chromatography has been applied 

Blends of poly(styrene-co-acrylonitrile) with polyethylene-co-propylene-co-diene have been characterised by SEC with UV and refractive index detectors, which allowed for the determination of average blend composition as a function of elution volume, and by precipitation LC, which allowed for complete separation of the blend components [112]. 

PAL has been used to study both miscible and immiscible polymer blends [41, 61, 67-70], PAL results have shown both positive and negative deviations from additivity of free volume with blend composition. In the case of multi phase systems, PAL data analysis is complicated by the fact that Ps may diffuse between the different blend phases. 

After an efficient initial Monte Carlo equilibration with chain scission and fusion moves, the diffusion of binary liquid blends of n-alkanes and polymers was investigated for chain lengths of C5/C78, C10/C78, and using molecular 

Asn-51 (gray) and Met-54 (green). The DNA is shown as a wireframe model. Positions of interfacial water molecules are given by dark blue spheres. After Reference [204]. 

Further results of all-atom molecular dynamics simulations have also been reported for PEO/PMMA blends [214], POSS/PE blends [215], blends of hydroxyl-terminated polybutadiene with explosive plasticizers [217], as well as a novel force field for PDMS and mixtures with alkanes [216]. The simulation of multiphase polymer systems has also been reviewed [208]. 

Because the knowledge of how to achieve certain polymer characteristics by blending is often considered a trade secret by processors, it is not often discussed or even mentioned by converters. There has been considerable research about the properties of blends, but often there is little information available about the composition of commercially available blends, making it difficult to tie theory to practice. 

Mixing of polymers either df melts or from solution are old techniques for obtaining specific mechanical or physical properties. The intermediate thermomechanical properties obtained are frequently desirable for a particular process or end use. Aside from numerous qualitative studies, very little pertinent work has been reported on the thermophysical behavior of poly blends. 

DTA curves of commercial high and low molecular weight polyethylene, polyethylene-copolypropylene and polyamide blends as well as mixtures of polymers and low molecular weight compounds have been discussed by Ke (38). 

In addition to X-ray, density and infrared techniques, DTA is becoming increasingly popular in determining the degree of crystallinity of polymer samples 44, 251—255). In analogy to the concept of 

For polyethylene, a linear relationship between melt enthalpy and specific volume is obtained as shown in Fig. 42, regardless of what crystallization conditions were employed. 

From the slope and intersect of the line obtained in Fig. 42, Hendus and filers derived the following equation for polyethylene 

The very signifieant smoke suppression effect of the FeOOH in the blends is explained in terms of iron/chlorine compounds formed in situ. The maximum smoke suppression effect was obtained at a blend ehlorine content of about 20%. It was also shown that the char formation is directly related to smoke formation and suppression in these polymer blends. 

Molybdenum and zine eontaining compounds have been used as flame and smoke suppressants for a variety of polymers. These metal containing species normally act to assist the build-up of char on the pol mier surface. This ehar is presumed to be the main method of flame retardancy. Halogenated systems form a large proportion of the market for molybdenum and zinc compounds. 

Although it is known that molybdenum can be vaporised by heating with HCl or HBr, most of the metal remains in the char of the burned polymers that eontained the original fire retardant additive compounds. This is seen when char formation of PVC is increased when molybdenum is added at low levels. A char value of almost 10% with no additive becomes nearly 24% with 2 phr of M0O3. Over 90% of the molybdenum is found in the char. Likewise 63% of zinc from a zinc borate smoke suppressant remains in the char. This contrasts with just 5% of antimony found in char from a similar PVC compound containing antimony oxide. 

It would appear that the molybdenum acts as a kind of catalyst to convert PVC degradation species from becoming aromatic compounds (these bum to produce the familiar dense, dark smoke), into more linear aliphatic species or carbonaceous char. 

Smoke suppression in rigid PVC can also be accomplished by the utilisation of a copper and molybdenum complex. A binary mixture of cuprous oxide and molybdenum trioxide reduces total smoke production, the average extinction area and smoke production rate. Increased char is formed and a reduced level of flammability in the PVC. 

Basic Thermodynamics. Equilibrium-phase behavior of mixtures is governed by the free energy of mixing and how this quantity, consisting of enthalpic 

Kirk-Othmer Encyclopedia of Chemical Technology (4th Edition) 

Flory-Huggins Theory. The simplest quantitative model foi that iacludes the most essential elements needed foi polymer blends is 

M refer to the density and molecular weight of /, and R is the gas constant. For simplicity, we assume each component to be monodisperse mote complex expressions result when polydispersity is considered (6). This model also assumes the heat of mixing pet unit volume follows a van Laar-type relation where B is 

Some important conclusions can be learned from this simple model. First, it shows that does not depend on polymer molecular weight, 

Flory-Huggins Theory. The simplest quantitative model for AGmx that includes the most essential elements needed for polymer blends is the Flory-Huggins theory, originally developed for polymer solutions (3,4). It assumes the only contribution to the entropy of mixing is combinatorial in origin and is given by equation 3, for a unit volume of a mixture of polymers A. and B. Here, pt and 

When the interaction energy density is positive, equation 5 defines a critical temperature of the UCST type (Fig. la) that is a function of component molecular weights. The LCST-type phase diagram, quite common for polymer blends, is not predicted by this simple theory unless B is 

National Research Council Canada, Industrial Materials Institute, Boucherville, QC, Canada 

In this introductory chapter the basic information on polymer blends (with a special emphasis on the commercial alloys) is presented in the sequence (i) a historical perspective on the polymer science and technology, (ii) polymeric structures and nomenclature, (iii) fundamental concepts in polymer blend science, and (iv) evolution of polymer blends technology. 

The world production of plastics in 1900 was about 30,000 tons — in the year 2000 it is expected to reach 151 Mt. The projected saturation level on the global scale (an increase by a factor of ten) is expected to be reached in the middle of the 21st century. The rapidity of the plastics expansion can be best judged by comparing it with steel — aheady in 1992 the annual world production of plastics more than doubled in volume the world production of steel, and nearly tripled its value. Polymers are the fastest growing structural materials. It is noteworthy that the polymer blend segment of the plastics industry increases at a rate about three times higher than the whole. 

Polymers are classified as either natural that resulted from natural biosynthesis, or synthetic. The natural (polysaccharides, proteins, nucleic acids, natural rubbers, cellulose, lignin, etc.) have been used for tens of thousands of years. In Egypt the musical string instruments, papyrus for writing, and styrene [in a tree balsam] for embalming were used 3,000 BC. For millennia shellac has been used in Indian turnery [Chattopadhyaya, 1986]. The natural rubber was used by Olmecs at least 3000 years ago [Stuart, 1993]. 

The term synthetic polymer refers equally well to linear, saturated macromolecules (i.e., thermoplastics), to unsaturated polymers (i.e., rubbers), or to any substance based on crosslinkable monomers, macromers, or pre-polymers (i.e., thermosets). The focus of this handbook is on blends of thermoplastics made of predominantly saturated, linear macromolecules. 

Polypropylene + ethylene/propylene/diene rubber, PP + EPDM. Applications automotive parts, flexible tubes, sports goods, toys. 

Poly(acrylonitrile-co-butadiene-co-styrene) + polycarbonate, ABS + PC Poly(acrylonitrile-co-butadiene-co-acrylester) + polycarbonate ASA + PC poly(acrylo-nitrile-co-butadiene-co-styrene) + polyamide, ABS + PA. Applications semifinished goods, automotive parts, electronic parts, optical parts, houseware goods. 

Poly(vinyl chloride) + poly(vinyl chloride-co-acrylate), PVC + VC/A poly(vinyl chloride) + chlorinated polyethylene, PVC + PE- C, poly( vinyl chloride) + poly(acrylonitrile-co-butadiene-co-acrylester), PVC + ASA. Applications semifinished goods, foils, plates, profiles, pipes, fittings, gutters, window frames, door frames, panels, housings, bottles, blow molding, disks, blocking layers, fibers, fleeces, nets. 

Polycarbonate + poly(ethylene terephthalate), PC + PET polycarbonate -i- liquid crystal polymer, PC + 

LCP polycarbonate + poly(butylene terephthalate), PC + PBT. Applications optical devices, covering devices, panes, safety glasses, semifinished goods, houseware goods, compact discs, bottles. 

Poly(methyl methacrylate) + poIy(vinylidine fluoride) 

Poly(ethyl methacrylate) + poly(vinylidine fluoride) Copoly(raethyl methacrylate-methyl acrylate) blends Copoly(methyl methacrylate-ethyl acrylate) blends Copoly(methyl methacrylate-butyl acrylate) blends Copoiy(mefhyl methacrylate-butyl methacrylate) blends Polystyrene + polybutadiene Polystyrene + polyisoprene Polystyrene + poly(vinyl methyl ether) 

Polystyrene + poly(ethylene glycol) (oligomer mixtures) Polystyrene + poly(2,6-dimethyl 1,4-phenylene oxide) 

Polyisobutene -I- poly(propylene glycol) (oligomer mixtures) Poly(ethylene oxide) + poly(propylene oxide) (oligomer mixtures) Poly(propylene glycol -f poly(dimethyl siloxane) (oligomer mixtures) 

However, as much of the fundamental work, which dates back to the 1930s uses simple laminar shear flow models and Couette flow, it is apparent that there should be a niche for single screw extruders. This raises the question of how large is this niche  

In practical terms, polymer blends can be put into three categories  

1) Combinations which give properties that are better than might be expected from their individual properties. 

2) Combinations which offer a predictable but useful balance of properties at an economic cost. 

3) Useful materials which can result from homogenising difficult to separate mixed polymer scrap and waste. 

As mentioned above, P3ATs are also melt-processable. The melting/softening point of P3ATs depends on the chain length of the alkyl group [44] (table 4.) 

TABLE 4. Effect of the alkyl chain length on the melting point of poly(3-alkylthiophene) [44.  

The processability of the P3ATs implies that it is possible to obtain a wide variety of polymer blends or composites with conventional technology polymers such as polyethylene (PE), polystyrene (PS), poly(vinyl chloride) (PVC) and poly(ethylene vinyl 

P3 AT blends can be made conducting by doping. The conductivity of the blends can be varied from less than 10 to 1 S/cm by varying the P30T content, the doping time, the matrix polymer or a combination of all of those parameters. In the case of EVA/P30T 

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Finally, similar effects can be seen in miscible polymer blends where the surface tension correlates with the enrichment of the lower-energy component at the surface as monitored by x-ray photoelectron spectroscopy [104],... 

Flammiche A, Flourston D J, Pollock FI M, Reading M and Song M 1996 Scanning thermal microscopy sub-surface imaging, thermal mapping of polymer blends, localised calorimetry J. Vac. Sol. Technol. B 14 1486... 

Figure B3.6.1. Illustration of the wide span of length seale in a binary polymer blend. (See the text for fiirther explanation.)...

The binary polymer blend exliibits a second-order unmixing transition. Close to the critical temperature the... 

The general fomi of the expansion is dictated by very general synnnetry considerations the specific coefficients for the example of a polymer blend can be derived from the self-consistent field theory. For a... 

Figure B3.6.2. Local mterface position in a binary polymer blend. After averaging the interfacial profile over small lateral patches, the interface can be described by a single-valued function u r. (Monge representation). Thennal fluctuations of the local interface position are clearly visible. From Wemer et al [49].

Monte Carlo simulations, which include fluctuations, then yields Simulations of a coarse-grained polymer blend by Wemer et al find = 1 [49] in the strong segregation limit, in rather good... 

Figure B3.6.5. Phase diagram of a ternary polymer blend consisting of two homopolymers, A and B, and a synnnetric AB diblock copolymer as calculated by self-consistent field theory. All species have the same chain length A and the figure displays a cut tlirough the phase prism at%N= 11 (which corresponds to weak segregation). The phase diagram contains two homopolymer-rich phases A and B, a synnnetric lamellar phase L and asynnnetric lamellar phases, which are rich in the A component or rich in the B component ig, respectively. From Janert and Schick [68].

Muller M 1999 Misoibility behavior and single ohain properties in polymer blends a bond fluotuation model study Macromol. Theory Simul. 8 343... 

Esoobedo F A and de Pablo J J 1999 On the sealing of the oritioal solution temperature of binary polymer blends with ohain length Macromolecules 32 900... 

Taylor-Maranas J K, Debenedetti P G, Graessley W W and Kumar S K 1997 Compressibility effeots in neutron soattering by polymer blends Macromolecules 30 6943... 

Cm,ORINE OXYGEN ACIDS AND SADTS - DICm,ORINE MONOXIDE, HYPOCIMOROUS ACID, AND HYPOCID.ORI IES] (Vol 5) Nonmiscible polymer blends... 

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