Classifications

• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
  • C08J5/20—Manufacture of shaped structures of ion-exchange resins
  • C08J5/22—Films, membranes or diaphragms
  • C08J5/2206—Films, membranes or diaphragms based on organic and/or inorganic macromolecular compounds
  • C08J5/2218—Synthetic macromolecular compounds
  • C08J5/2256—Synthetic macromolecular compounds based on macromolecular compounds obtained by reactions other than those involving carbon-to-carbon bonds, e.g. obtained by polycondensation
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
  • B01J41/00—Anion exchange; Use of material as anion exchangers; Treatment of material for improving the anion exchange properties
  • B01J41/08—Use of material as anion exchangers; Treatment of material for improving the anion exchange properties
  • B01J41/12—Macromolecular compounds
  • B01J41/13—Macromolecular compounds obtained otherwise than by reactions only involving unsaturated carbon-to-carbon bonds
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D69/00—Semi-permeable membranes for separation processes or apparatus characterised by their form, structure or properties; Manufacturing processes specially adapted therefor
  • B01D69/02—Semi-permeable membranes for separation processes or apparatus characterised by their form, structure or properties; Manufacturing processes specially adapted therefor characterised by their properties
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/28—Polymers of vinyl aromatic compounds
  • B01D71/281—Polystyrene
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/30—Polyalkenyl halides
  • B01D71/32—Polyalkenyl halides containing fluorine atoms
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/52—Polyethers
  • B01D71/521—Aliphatic polyethers
  • B01D71/5211—Polyethylene glycol or polyethyleneoxide
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/52—Polyethers
  • B01D71/522—Aromatic polyethers
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/52—Polyethers
  • B01D71/522—Aromatic polyethers
  • B01D71/5222—Polyetherketone, polyetheretherketone, or polyaryletherketone
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D71/00—Semi-permeable membranes for separation processes or apparatus characterised by the material; Manufacturing processes specially adapted therefor
  • B01D71/06—Organic material
  • B01D71/66—Polymers having sulfur in the main chain, with or without nitrogen, oxygen or carbon only
  • B01D71/68—Polysulfones; Polyethersulfones
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01J—CHEMICAL OR PHYSICAL PROCESSES, e.g. CATALYSIS OR COLLOID CHEMISTRY; THEIR RELEVANT APPARATUS
  • B01J41/00—Anion exchange; Use of material as anion exchangers; Treatment of material for improving the anion exchange properties
  • B01J41/08—Use of material as anion exchangers; Treatment of material for improving the anion exchange properties
  • B01J41/12—Macromolecular compounds
  • B01J41/14—Macromolecular compounds obtained by reactions only involving unsaturated carbon-to-carbon bonds
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J5/00—Manufacture of articles or shaped materials containing macromolecular substances
  • C08J5/20—Manufacture of shaped structures of ion-exchange resins
  • C08J5/22—Films, membranes or diaphragms
  • C08J5/2206—Films, membranes or diaphragms based on organic and/or inorganic macromolecular compounds
  • C08J5/2218—Synthetic macromolecular compounds
  • C08J5/2231—Synthetic macromolecular compounds based on macromolecular compounds obtained by reactions involving unsaturated carbon-to-carbon bonds
• • C—CHEMISTRY; METALLURGY
  • C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
  • C25B—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES FOR THE PRODUCTION OF COMPOUNDS OR NON-METALS; APPARATUS THEREFOR
  • C25B13/00—Diaphragms; Spacing elements
  • C25B13/04—Diaphragms; Spacing elements characterised by the material
  • C25B13/08—Diaphragms; Spacing elements characterised by the material based on organic materials
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
  • H01M8/1025—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having only carbon and oxygen, e.g. polyethers, sulfonated polyetheretherketones [S-PEEK], sulfonated polysaccharides, sulfonated celluloses or sulfonated polyesters
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
  • H01M8/103—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having nitrogen, e.g. sulfonated polybenzimidazoles [S-PBI], polybenzimidazoles with phosphoric acid, sulfonated polyamides [S-PA] or sulfonated polyphosphazenes [S-PPh]
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/10—Fuel cells with solid electrolytes
  • H01M8/1016—Fuel cells with solid electrolytes characterised by the electrolyte material
  • H01M8/1018—Polymeric electrolyte materials
  • H01M8/102—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer
  • H01M8/1032—Polymeric electrolyte materials characterised by the chemical structure of the main chain of the ion-conducting polymer having sulfur, e.g. sulfonated-polyethersulfones [S-PES]
• • H—ELECTRICITY
  • H01—ELECTRIC ELEMENTS
  • H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
  • H01M8/00—Fuel cells; Manufacture thereof
  • H01M8/18—Regenerative fuel cells, e.g. redox flow batteries or secondary fuel cells
  • H01M8/184—Regeneration by electrochemical means
  • H01M8/188—Regeneration by electrochemical means by recharging of redox couples containing fluids; Redox flow type batteries
• • B—PERFORMING OPERATIONS; TRANSPORTING
  • B01—PHYSICAL OR CHEMICAL PROCESSES OR APPARATUS IN GENERAL
  • B01D—SEPARATION
  • B01D2325/00—Details relating to properties of membranes
  • B01D2325/42—Ion-exchange membranes
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2325/00—Characterised by the use of homopolymers or copolymers of compounds having one or more unsaturated aliphatic radicals, each having only one carbon-to-carbon double bond, and at least one being terminated by an aromatic carbocyclic ring; Derivatives of such polymers
  • C08J2325/18—Homopolymers or copolymers of aromatic monomers containing elements other than carbon and hydrogen
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2471/00—Characterised by the use of polyethers obtained by reactions forming an ether link in the main chain; Derivatives of such polymers
  • C08J2471/02—Polyalkylene oxides
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2479/00—Characterised by the use of macromolecular compounds obtained by reactions forming in the main chain of the macromolecule a linkage containing nitrogen with or without oxygen, or carbon only, not provided for in groups C08J2461/00 - C08J2477/00
  • C08J2479/04—Polycondensates having nitrogen-containing heterocyclic rings in the main chain; Polyhydrazides; Polyamide acids or similar polyimide precursors
• • C—CHEMISTRY; METALLURGY
  • C08—ORGANIC MACROMOLECULAR COMPOUNDS; THEIR PREPARATION OR CHEMICAL WORKING-UP; COMPOSITIONS BASED THEREON
  • C08J—WORKING-UP; GENERAL PROCESSES OF COMPOUNDING; AFTER-TREATMENT NOT COVERED BY SUBCLASSES C08B, C08C, C08F, C08G or C08H
  • C08J2481/00—Characterised by the use of macromolecular compounds obtained by reactions forming in the main chain of the macromolecule a linkage containing sulfur with or without nitrogen, oxygen, or carbon only; Polysulfones; Derivatives of such polymers
  • C08J2481/06—Polysulfones; Polyethersulfones

Definitions

• AEMs anion exchange membranes
• APEFCs alkaline polymer electrolyte fuel cells
• AEE alkaline polymer electrolyte electrolysis
• RFBs redox flow batteries
• RED Reverse electrodialysis
• MFCs microwave fuel cells
• DD diffusion dialysis
• a major advantage of using AEM in electrochemical conversion processes such as fuel cells or electrolysis is that when using AEMs for the electrocatalytic reactions at the electrodes no precious metal catalysts consisting of platinum group metals (PGM) are required, thus containing AEM Membrane electrode assemblies (MEAs) are significantly less expensive than cation exchange membrane (CEM) containing MEAs.
• PGM platinum group metals
• AEMs have the following major drawbacks compared to CEMs:
• Ion conductivity is significantly lower for most AEM types than for CEMs of comparable ion exchange capacity (IEC), in part because most of the AEMs have a hydrocarbon backbone that is significantly less hydrophobic than perfluorinated ones, for example Polymer backbone of perfluorinated membranes of the Nafion ® type, so that it comes in the AEM to a lower separation between ionic groups and polymer backbone, which leads to lower ionic conductivity because of the then lower local density of the anion exchange groups, especially for most AEM types the Festkationen merely attached to the polymer backbone via a CH 2 bridge [20].
• IEC ion exchange capacity
• AEM A monomer having aromatic groups
• polystyrene polystyrene
• polyphenylene ethers or other aromatic polyethers
• polyethersulfones polyether ketones o. ⁇ .
• the first step in the preparation of AEM is the synthesis of a polymer with halomethyl side groups.
• Halomethylation is achieved by (1) chloro- or bromomethylation with hydrogen, formaldehyde and a Lewis acid such as ZnCl 2 or AICI 3 (Blanc reaction [23,24]), or (2) bromination of the CH 3 side group of aromatic polymers with N-bromo-succinimide (NBS) by the well-Ziegler bromination reaction [25].
• the Blanc reaction is associated with the appearance of the highly carcinogenic by-product bis (chloromethyl) ether. For this reason, the Wohl-Ziegler reaction is now preferably used in the production of halomethylated aromatic polymers.
• Literature examples for the preparation of bromomethylated aromatic polymers by the Wohl-Ziegler reaction are the bromomethylation of polyphenylene oxide [26] or the bromomethylation of a methylated polyethersulfone [27].
• Phase-segregated AEMs with improved ionic conductivity are obtainable by the preparation of linear block copolymers from hydrophobic and ionic blocks [31] or by graft copolymers with an anion exchange group-containing grafting side chain [32] (example: grafting of vinylbenzyl chloride side chains onto e " irradiated ETFE, and quaternization of the chloromethylated side chains with trimethylamine [33]).
• a sterically hindered chemically stabilized cationic functional group is the tris (2,4,6-trimethoxyphenyl) phosphonium cation [40], which was attached to polyvinylbenzyl chloride graft chains after storage for 75 hours in IN NaOH at 60 ° C had no degradation.
• a positively charged bis (terpyridine) ruthenium (II) complex was attached to a norbornene polymer [41].
• the AEM thus prepared showed excellent stability in an alkaline environment: incorporation of the polymer in IN NaOH at room temperature showed no degradation even after half a year.
• AK ionically and covalently cross-linked AEM blends from bromomethylated PPO or a bromomethylated and partially fluorinated arylene main chain polymer and a partially fluorinated PBI (FePBI) as a mechanically and chemically stable matrix and a sulfonated polyethersulfone sPPSU added in excess [46].
• the halomethylated blend component was quaternized with N-methylmorpholine (NMM) to form the anion exchange group [47].
• AEMs were synthesized consisting of rigid / flexible semi-interpenetrating networks of triethylamine quaternized PPO and a polyethylene glycol network. It was found that this AEM has high ionic conductivity ( ⁇ 0 ⁇ - up to 80 mS / cm) and a high alkali stability (degradation of ionic conductivity between 25 and 30% within 30 days of storage in IM NaOH at 80 ° C) [52].
• polyethylene glycols were grafted onto chloromethylated SEBS polymers and the resulting copolymers were then quaternized with trimethylamine.
• the resulting AEMs showed very high mechanical and chemical stabilities in 2.5M KOH at 60 ° C (increasing the ionic conductivity during storage in the KOH from 20 to 24 mS / cm) and high ionic conductivities ( ⁇ 0 ⁇ - up to 52 mS / cm) to [53].
• anion-exchange blend membranes of the following blend components are present in anion-exchange blend membranes of the following blend components:
• x 0-12, for example chloromethylated polystyrene or bromomethylated polyphenylene oxide;
• sterically hindered tertiary nitrogen compounds are:
• halomethylated polymers 1, 2-dimethyl-4,5-diphenyl-1H-imidazoles
• Bromomethylated partially fluorinated aromatic polyether II a matrix polymer, for example, a basic polybenzimidazole;
• a matrix polymer for example, a basic polybenzimidazole;
• Examples of basic matrix polymers are:
• a sulfonated aryl polymer as an ionic macromolecular crosslinker (ionic crosslinking with the basic functional groups of the matrix polymer and with the anion exchange groups of the quaternized halomethylated polymer.
• sulfonated aryl polymers examples include sulfonation SFS001)
• sulfonated aromatic poly (phenylphosphine oxide) II optionally a sulfonated polymer as a covalent macromolecular crosslinker whose sulfinate groups undergo covalent crosslinking via the sulfinate-S-alkylation with the halomethyl groups of the halomethylated polymer.
• a covalent crosslinking reaction between a sulfonated aromatic poly (phenylphosphine oxide) II optionally a sulfonated polymer as a covalent macromolecular crosslinker whose sulfinate groups undergo covalent crosslinking via the sulfinate-S-alkylation with the halomethyl groups of the halomethylated polymer.
• the membrane properties such as conductivity and thermal and chemical stability, in particular stability in strongly alkaline solutions, such as aqueous potassium hydroxide solution or sodium hydroxide solution
• the sulfinate groups of the sulfinated polymer with epoxy or halomethyl end groups of the polyethylene glycol are capable of reaction, presumably under sulfinate S-alkylation of the sulfinate groups by the epoxide or halomethyl groups.
• the reaction of the sulfinate groups of the sulfinated polymer with the epoxide end groups of the polyethylene glycol are shown below:
• anion-exchange blend membranes AEBM
• polymeric blend components halomethylated polymer, matrix polymer (eg.
• Polybenzimidazole polyethylene glycol with epoxide or halomethyl end groups, optionally sulfonated polymer and / or sulfinated polymer) are together in a dipoiar-aprotic solvent or in a mixture of different dipoiar-aprotic solvents (examples: ⁇ , ⁇ -dimethylacetamide, N-methylpyrrolidinone, N-ethyl pyrrolidinone, dimethyl sulfoxide sulfolane).
• the polymer solutions are doctored or cast on a support (glass plate, metal plate, plastic film, etc.), and the solvent is evaporated in a circulating air dryer or a vacuum oven at temperatures between room temperature and 150 ° C.
• Polybenzimidazole polyethylene glycol with epoxide or halomethyl end groups, optionally sulfonated polymer and / or sulfinated polymer) are together in a dipoiar-aprotic solvent or in a mixture of different dipoiar-aprotic solvents (examples: ⁇ , ⁇ -dimethylacetamide, N-methylpyrrolidinone, N-ethyl pyrrolidinone, dimethyl sulfoxide sulfolane).
• the tertiary amine or the N-monoalkylated (benz) imidazole or N-monoalkylated pyrazole is added to the solution .
• the polymer solutions are doctored or cast on a support (glass plate, metal plate, plastic film, etc.), and the solvent is evaporated in a circulating air dryer or a vacuum oven at temperatures between room temperature and 150 ° C.
• Figure 1 shows the chloride conductivities of the membranes 2175 and 2176 in the temperature range between 30 and 90 ° C with a constant relative humidity of 90%.
• Figure 2 shows the chloride conductivity of the membrane 2176 before and after 10, 20 and 30 days of incorporation in IM KOH in a temperature range of 30 to 90 ° C and a relative humidity of 90%.
• Figure 3 shows the TGA curves of membranes 2175 and 2176 before and after 10 days treatment in IM KOH at 90 ° C
• Figure 4 shows the TGA curves of membrane 2176 before and after 10, 20 and 30 days treatment in IM KOH at 90 ° C
• Figure 5 shows the chloride conductivity of the membrane 2190A before and after 10 days storage in IM KOH in the temperature range 30-90 ° C at a relative humidity of 90%
• Figure 6 shows the TGA curves of membrane 2190A before and after 10 days of storage in IM KOH at 90 ° C
• Figure 7 shows the chloride conductivity of membrane 2215 before and after 10 days storage in IM KOH in the temperature range 30-90 ° C at a relative humidity of 90%
• Figure 8 shows the TGA curves of membrane 2215 before and after 10 days storage in IM KOH at 90 ° C
• Figure 9 shows the chloride conductivity of the membrane 2179B before and after 10 days storage in IM KOH in the temperature range 30-90 ° C at a relative humidity of 90%
• Figure 10 shows the chloride conductivity of membrane 2216 before and after 10 days storage in IM KOH in the temperature range 30-90 ° C at a relative humidity of 90%
• Figure 11 shows the chloride conductivity of the commercial anion exchange membrane Tokuyama A201 in the temperature range 30-80 ° C at a relative humidity of 90%
• membrane 2175 0.25 g of epoxide-terminated polyethylene glycol (molecular mass 500 daltons, ALDRICH product no. 475696) are added to this mixture after homogenization, in the case of membrane 2176 0.25 g of epoxide-terminated polyethylene glycol (Molecular mass 6000 daltons, ALDRICH product no. 731803).
• the polymer solutions are doctored on a glass plate. Thereafter, the solvent is evaporated in a convection oven at 130 ° C for a period of 2 hours. The polymer films are then removed under water and after-treated as follows: at 60 ° C for 24 hours in a 10% strength by weight solution of tetramethylimidazole in ethanol
• Membrane 2175 ion exchange capacity before / after KOH treatment * [meq OH ⁇ / g membrane]: 2.92 / 2.96
• Membrane 2176 ion exchange capacity before / after KOH treatment * [meq OH ⁇ / g membrane]:
• FIG. 2 shows the chloride conductivities of the membrane 2176 before and after 10, 20 and 30 days incorporation in IM KOH in the temperature range from 30 to 90 ° C.
• TGA curves of the 2176 were recorded before and after 10, 20 and 30 days of incorporation in KOH. These TGA curves are shown in Figure 4. From Figure 4, it can be seen that the TGA curves of all 4 samples are nearly congruent up to a temperature of about 430 ° C, from which one can conclude that the 2176 still shows no sign of significant degradation even after 30 days of incorporation into KOH which confirms the results of the conductivity tests.
• Application Example 2 AEM blend of PVBCI, PBIOO, a sulfonated polyethersulfone (SAC098, see description), tetramethylimidazole for quaternizing the PVBCI and an epoxide-terminated polyethylene glycol having a lower AEM content than in Application Example 1 but the same molar ratio between PBIOO and PEG -Diepoxid 6000 (Membrane MJK2190A)
• epoxide-terminated polyethylene glycol molecular mass 6000 daltons, ALDRICH product no. 731803
• the polymer solution is doctored onto a glass plate. Thereafter, the solvent is evaporated in a convection oven at 130 ° C for a period of 2 hours.
• the polymer film is then removed under water and after-treated as follows: at 60 ° C for 24 hours in a 10 wt% solution of tetramethylimidazole in ethanol
• Part of the membrane is placed in an aqueous IM KOH solution for a period of 10 days at a temperature of 90 ° C.
• the chloride conductivity was also determined in this membrane as a function of the temperature between 30 and 90 ° C at a relative humidity of 90%.
• the conductivity curves are shown in Figure 5.
• the conductivity of the 2190A membrane also increases during KOH treatment.
• TGA curves of the membrane were recorded before and after 10 days of KOH treatment.
• the TGA curves are shown in Figure 6. Even with this membrane, the TGA curves before and after 10 days of KOH treatment almost congruent, at least up to a temperature of about 350 ° C, what indicates that after 10 days of incorporation in IM KOH at 90 ° C, no significant degradation of the membranes has yet occurred.
• the solvent is evaporated in a convection oven at 140 ° C for a period of 2 hours.
• the polymer film is then removed under water and after-treated as follows: at 60 ° C for 24 hours in a 10 wt% solution of tetramethylimidazole in ethanol
• Part of the membrane is placed in an aqueous IM KOH solution for a period of 10 days at a temperature of 90 ° C *
• the chloride conductivity was also determined in this membrane as a function of the temperature between 30 and 90 ° C at a relative humidity of 90%.
• the conductivity curves are shown in Figure 7.
• the chloride conductivity after lOd storage in IM KOH at 90 ° C is higher than before.
• TGA curves of the membrane were recorded before and after 10 days of KOH treatment. The TGA curves are shown in Figure 8.
• the TGA curves before and after 10 days KOH treatment almost congruent, at least up to a temperature of about 350 ° C, indicating that after 10 days of incorporation in IM KOH at 90 ° C, no significant Degradation of the membranes has taken place.
• Comparative Example 1 AEM blend of PVBCI, PBIOO, a sulfonated polyethersulfone (SAC098, see description), tetramethylimidazole for quaternization of the PVBCI with the same calculated IEC as the membranes MJK2175 and MJK2176, but without PEG diglycidyl ether (membrane 2179B)
• the polymer solutions are doctored on a glass plate. Thereafter, the solvent is evaporated in a convection oven at 140 ° C for a period of 2 hours.
• the polymer films are then dissolved in water and after-treated as follows: at 60 ° C for 24 hours in a 10 wt% solution of tetramethylimidazole in ethanol
• Parts of the membranes are placed in an aqueous IM KOH solution for a period of 10 days at a temperature of 90 ° C *
• Water uptake is significantly lower than at 2175 and 2176. This can be explained by the lower hydrophilicity of the control membrane.
• the impedance of the 2179B was higher in conductivity measurement at room temperature and in 0.5N NaCl as at 2175 and 2176 after the KOH treatment, the impedance of the 2179B again became function of the temperature at a relative humidity of 90 % measured.
• the conductivity curve of the 2179B under these conditions is shown in Figure 9.
• the chloride conductivity is much lower than that of the 2175 and 2176 containing a PEG phase, and the impedance after the KOH treatment is significantly lower than before.
• the solvent is evaporated in a convection oven at 140 ° C for a period of 2 hours.
• the polymer film is then removed under water and after-treated as follows: at 60 ° C for 24 hours in a 10 wt% solution of tetramethylimidazole in ethanol
• Portions of the membranes are placed in an aqueous IM KOH solution for a period of 10 days at a temperature of 90 ° C
• the cr conductivity at room temperature in 0.5N NaCl is significantly lower than in the case of the membrane 2215 according to the invention. This shows the positive influence that the addition of a hydrophilic PEG phase has to the membrane.
• the water uptake is significantly lower than at 2215. This can be explained by the lower hydrophilicity of the control membrane. Since the Cl " conductivity of the 2216 was higher at the room temperature and 0.5N NaCl than at 2215 after the KOH treatment, the impedance of the 2215 again became 90% relative to the temperature at a relative humidity of 90%. The conductivity curve of the 2215 under these conditions is shown in Figure 10.
• Comparative Example 3 Commercial anion exchange membrane A201 (development code A006) of the manufacturer Tokuyama
• This membrane is company secret.
• the anion exchange group of this membrane is the trimethylammonium group. But it is obviously a cross-linked membrane because the extraction of the membrane gave a gel content of 95%.
• this membrane is company secret. But it is obviously a cross-linked membrane, as the extraction of the membrane gave a gel content of 93.3%.
• the chloride conductivity of this membrane is substantially lower than that of most of the membranes of this invention listed as examples, which u. A. is also because this membrane is fabric reinforced.

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• 2016
  • 2016-06-22 DE DE102016007815.4A patent/DE102016007815A1/de not_active Withdrawn
• 2017
  • 2017-06-22 EP EP17767982.6A patent/EP3478750A1/de active Pending
  • 2017-06-22 JP JP2019520195A patent/JP2019522887A/ja active Pending
  • 2017-06-22 US US16/312,975 patent/US11278879B2/en active Active
  • 2017-06-22 DE DE112017003141.9T patent/DE112017003141A5/de not_active Withdrawn
  • 2017-06-22 AU AU2017280451A patent/AU2017280451A1/en not_active Abandoned
  • 2017-06-22 WO PCT/DE2017/000179 patent/WO2017220065A1/de unknown
• 2022
  • 2022-03-21 US US17/700,325 patent/US20220212183A1/en active Pending
  • 2022-07-01 JP JP2022107354A patent/JP2022160413A/ja active Pending

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