CA2567127C - High stability flow-through non-carbon anodes for aluminium electrowinning - Google Patents
High stability flow-through non-carbon anodes for aluminium electrowinning Download PDFInfo
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- CA2567127C CA2567127C CA2567127A CA2567127A CA2567127C CA 2567127 C CA2567127 C CA 2567127C CA 2567127 A CA2567127 A CA 2567127A CA 2567127 A CA2567127 A CA 2567127A CA 2567127 C CA2567127 C CA 2567127C
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- Prior art keywords
- cell
- anode
- layer
- cobalt
- coo
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- 239000004411 aluminium Substances 0.000 title claims abstract description 65
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 65
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 64
- 238000005363 electrowinning Methods 0.000 title claims abstract description 45
- 229910052799 carbon Inorganic materials 0.000 title claims abstract description 22
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 title claims abstract description 18
- IVMYJDGYRUAWML-UHFFFAOYSA-N cobalt(ii) oxide Chemical compound [Co]=O IVMYJDGYRUAWML-UHFFFAOYSA-N 0.000 claims abstract description 144
- 239000003792 electrolyte Substances 0.000 claims abstract description 126
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 72
- 239000001301 oxygen Substances 0.000 claims abstract description 72
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 claims abstract description 61
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 claims abstract description 37
- 229910052751 metal Inorganic materials 0.000 claims abstract description 34
- 239000002184 metal Substances 0.000 claims abstract description 34
- 229910000428 cobalt oxide Inorganic materials 0.000 claims abstract description 30
- 238000005868 electrolysis reaction Methods 0.000 claims abstract description 23
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 claims abstract description 10
- 239000010410 layer Substances 0.000 claims description 171
- 239000010941 cobalt Substances 0.000 claims description 92
- 229910017052 cobalt Inorganic materials 0.000 claims description 91
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 claims description 90
- PXHVJJICTQNCMI-UHFFFAOYSA-N Nickel Chemical compound [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 claims description 70
- 239000000758 substrate Substances 0.000 claims description 39
- 229910052759 nickel Inorganic materials 0.000 claims description 36
- 230000003647 oxidation Effects 0.000 claims description 31
- 238000007254 oxidation reaction Methods 0.000 claims description 31
- KLZUFWVZNOTSEM-UHFFFAOYSA-K Aluminium flouride Chemical compound F[Al](F)F KLZUFWVZNOTSEM-UHFFFAOYSA-K 0.000 claims description 30
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 30
- UPWOEMHINGJHOB-UHFFFAOYSA-N oxo(oxocobaltiooxy)cobalt Chemical compound O=[Co]O[Co]=O UPWOEMHINGJHOB-UHFFFAOYSA-N 0.000 claims description 28
- 229910052715 tantalum Inorganic materials 0.000 claims description 27
- 239000011248 coating agent Substances 0.000 claims description 26
- 238000000576 coating method Methods 0.000 claims description 26
- GUVRBAGPIYLISA-UHFFFAOYSA-N tantalum atom Chemical compound [Ta] GUVRBAGPIYLISA-UHFFFAOYSA-N 0.000 claims description 25
- 229910052758 niobium Inorganic materials 0.000 claims description 22
- 239000010955 niobium Substances 0.000 claims description 22
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 22
- WFKWXMTUELFFGS-UHFFFAOYSA-N tungsten Chemical compound [W] WFKWXMTUELFFGS-UHFFFAOYSA-N 0.000 claims description 22
- 229910052721 tungsten Inorganic materials 0.000 claims description 22
- 239000010937 tungsten Substances 0.000 claims description 22
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 21
- 229910052750 molybdenum Inorganic materials 0.000 claims description 21
- 239000011733 molybdenum Substances 0.000 claims description 21
- 239000000463 material Substances 0.000 claims description 19
- -1 oxygen ions Chemical class 0.000 claims description 19
- 230000004888 barrier function Effects 0.000 claims description 16
- 239000010949 copper Substances 0.000 claims description 16
- NROKBHXJSPEDAR-UHFFFAOYSA-M potassium fluoride Chemical compound [F-].[K+] NROKBHXJSPEDAR-UHFFFAOYSA-M 0.000 claims description 16
- 229910000531 Co alloy Inorganic materials 0.000 claims description 15
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 14
- 229910045601 alloy Inorganic materials 0.000 claims description 14
- 239000000956 alloy Substances 0.000 claims description 14
- 229910052802 copper Inorganic materials 0.000 claims description 14
- 229910052742 iron Inorganic materials 0.000 claims description 14
- 239000011698 potassium fluoride Substances 0.000 claims description 13
- PUZPDOWCWNUUKD-UHFFFAOYSA-M sodium fluoride Chemical compound [F-].[Na+] PUZPDOWCWNUUKD-UHFFFAOYSA-M 0.000 claims description 12
- 239000011241 protective layer Substances 0.000 claims description 11
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 claims description 10
- 229910001634 calcium fluoride Inorganic materials 0.000 claims description 10
- PQXKHYXIUOZZFA-UHFFFAOYSA-M lithium fluoride Chemical compound [Li+].[F-] PQXKHYXIUOZZFA-UHFFFAOYSA-M 0.000 claims description 10
- 150000002739 metals Chemical class 0.000 claims description 10
- BASFCYQUMIYNBI-UHFFFAOYSA-N platinum Chemical compound [Pt] BASFCYQUMIYNBI-UHFFFAOYSA-N 0.000 claims description 10
- 229910052710 silicon Inorganic materials 0.000 claims description 10
- 239000010703 silicon Substances 0.000 claims description 10
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims description 9
- 150000001875 compounds Chemical class 0.000 claims description 9
- 239000000470 constituent Substances 0.000 claims description 9
- 239000000203 mixture Substances 0.000 claims description 9
- 239000011148 porous material Substances 0.000 claims description 9
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 8
- 229910052804 chromium Inorganic materials 0.000 claims description 8
- 239000011651 chromium Substances 0.000 claims description 8
- 239000002019 doping agent Substances 0.000 claims description 8
- 239000002245 particle Substances 0.000 claims description 8
- 235000003270 potassium fluoride Nutrition 0.000 claims description 8
- 238000000034 method Methods 0.000 claims description 7
- 239000000654 additive Substances 0.000 claims description 6
- 235000013024 sodium fluoride Nutrition 0.000 claims description 6
- 239000011775 sodium fluoride Substances 0.000 claims description 6
- 150000001785 cerium compounds Chemical class 0.000 claims description 5
- 229910052697 platinum Inorganic materials 0.000 claims description 5
- UQSXHKLRYXJYBZ-UHFFFAOYSA-N Iron oxide Chemical compound [Fe]=O UQSXHKLRYXJYBZ-UHFFFAOYSA-N 0.000 claims description 4
- KDLHZDBZIXYQEI-UHFFFAOYSA-N Palladium Chemical compound [Pd] KDLHZDBZIXYQEI-UHFFFAOYSA-N 0.000 claims description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 4
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 4
- XJHCXCQVJFPJIK-UHFFFAOYSA-M caesium fluoride Chemical compound [F-].[Cs+] XJHCXCQVJFPJIK-UHFFFAOYSA-M 0.000 claims description 4
- 229910052735 hafnium Inorganic materials 0.000 claims description 4
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims description 4
- 229910001635 magnesium fluoride Inorganic materials 0.000 claims description 4
- AHLATJUETSFVIM-UHFFFAOYSA-M rubidium fluoride Chemical compound [F-].[Rb+] AHLATJUETSFVIM-UHFFFAOYSA-M 0.000 claims description 4
- 229910052719 titanium Inorganic materials 0.000 claims description 4
- 239000010936 titanium Substances 0.000 claims description 4
- 229910052720 vanadium Inorganic materials 0.000 claims description 4
- GPPXJZIENCGNKB-UHFFFAOYSA-N vanadium Chemical compound [V]#[V] GPPXJZIENCGNKB-UHFFFAOYSA-N 0.000 claims description 4
- 229910052726 zirconium Inorganic materials 0.000 claims description 4
- 229910000640 Fe alloy Inorganic materials 0.000 claims description 3
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 3
- 229910052748 manganese Inorganic materials 0.000 claims description 3
- 239000011572 manganese Substances 0.000 claims description 3
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims description 3
- 239000002243 precursor Substances 0.000 claims description 3
- 229910052727 yttrium Inorganic materials 0.000 claims description 3
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 3
- 229910052725 zinc Inorganic materials 0.000 claims description 3
- 239000011701 zinc Substances 0.000 claims description 3
- 229910000881 Cu alloy Inorganic materials 0.000 claims description 2
- 229910001122 Mischmetal Inorganic materials 0.000 claims description 2
- 229910000990 Ni alloy Inorganic materials 0.000 claims description 2
- KJTLSVCANCCWHF-UHFFFAOYSA-N Ruthenium Chemical compound [Ru] KJTLSVCANCCWHF-UHFFFAOYSA-N 0.000 claims description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 2
- 230000000996 additive effect Effects 0.000 claims description 2
- OYLGJCQECKOTOL-UHFFFAOYSA-L barium fluoride Chemical compound [F-].[F-].[Ba+2] OYLGJCQECKOTOL-UHFFFAOYSA-L 0.000 claims description 2
- 229910001632 barium fluoride Inorganic materials 0.000 claims description 2
- QCCDYNYSHILRDG-UHFFFAOYSA-K cerium(3+);trifluoride Chemical compound [F-].[F-].[F-].[Ce+3] QCCDYNYSHILRDG-UHFFFAOYSA-K 0.000 claims description 2
- 229910052741 iridium Inorganic materials 0.000 claims description 2
- GKOZUEZYRPOHIO-UHFFFAOYSA-N iridium atom Chemical compound [Ir] GKOZUEZYRPOHIO-UHFFFAOYSA-N 0.000 claims description 2
- 229910052747 lanthanoid Inorganic materials 0.000 claims description 2
- 150000002602 lanthanoids Chemical class 0.000 claims description 2
- ORUIBWPALBXDOA-UHFFFAOYSA-L magnesium fluoride Chemical compound [F-].[F-].[Mg+2] ORUIBWPALBXDOA-UHFFFAOYSA-L 0.000 claims description 2
- 229910052763 palladium Inorganic materials 0.000 claims description 2
- 229910052703 rhodium Inorganic materials 0.000 claims description 2
- 239000010948 rhodium Substances 0.000 claims description 2
- MHOVAHRLVXNVSD-UHFFFAOYSA-N rhodium atom Chemical compound [Rh] MHOVAHRLVXNVSD-UHFFFAOYSA-N 0.000 claims description 2
- 229910052707 ruthenium Inorganic materials 0.000 claims description 2
- FVRNDBHWWSPNOM-UHFFFAOYSA-L strontium fluoride Chemical compound [F-].[F-].[Sr+2] FVRNDBHWWSPNOM-UHFFFAOYSA-L 0.000 claims description 2
- 229910001637 strontium fluoride Inorganic materials 0.000 claims description 2
- 239000011135 tin Substances 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- 238000009736 wetting Methods 0.000 claims description 2
- 239000011149 active material Substances 0.000 claims 1
- FEBJSGQWYJIENF-UHFFFAOYSA-N nickel niobium Chemical compound [Ni].[Nb] FEBJSGQWYJIENF-UHFFFAOYSA-N 0.000 claims 1
- UBEWDCMIDFGDOO-UHFFFAOYSA-N cobalt(II,III) oxide Inorganic materials [O-2].[O-2].[O-2].[O-2].[Co+2].[Co+3].[Co+3] UBEWDCMIDFGDOO-UHFFFAOYSA-N 0.000 description 23
- 230000000052 comparative effect Effects 0.000 description 18
- 230000015572 biosynthetic process Effects 0.000 description 13
- 238000006243 chemical reaction Methods 0.000 description 12
- 238000004090 dissolution Methods 0.000 description 12
- 229910001610 cryolite Inorganic materials 0.000 description 10
- 238000004070 electrodeposition Methods 0.000 description 9
- 238000004519 manufacturing process Methods 0.000 description 9
- 238000009792 diffusion process Methods 0.000 description 8
- 239000007789 gas Substances 0.000 description 7
- 230000001965 increasing effect Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 6
- 230000007797 corrosion Effects 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 6
- 238000012360 testing method Methods 0.000 description 6
- 239000010405 anode material Substances 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 238000003466 welding Methods 0.000 description 5
- XVVDIUTUQBXOGG-UHFFFAOYSA-N [Ce].FOF Chemical compound [Ce].FOF XVVDIUTUQBXOGG-UHFFFAOYSA-N 0.000 description 4
- 239000002002 slurry Substances 0.000 description 4
- 239000002344 surface layer Substances 0.000 description 4
- LYCAIKOWRPUZTN-UHFFFAOYSA-N Ethylene glycol Chemical compound OCCO LYCAIKOWRPUZTN-UHFFFAOYSA-N 0.000 description 3
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 3
- XLJKHNWPARRRJB-UHFFFAOYSA-N cobalt(2+) Chemical compound [Co+2] XLJKHNWPARRRJB-UHFFFAOYSA-N 0.000 description 3
- 230000001427 coherent effect Effects 0.000 description 3
- 239000004020 conductor Substances 0.000 description 3
- 230000003247 decreasing effect Effects 0.000 description 3
- 239000011737 fluorine Substances 0.000 description 3
- 229910052731 fluorine Inorganic materials 0.000 description 3
- 238000011065 in-situ storage Methods 0.000 description 3
- 238000002161 passivation Methods 0.000 description 3
- 230000002829 reductive effect Effects 0.000 description 3
- 230000000007 visual effect Effects 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 239000002253 acid Substances 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 238000009826 distribution Methods 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000002708 enhancing effect Effects 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- ZSIAUFGUXNUGDI-UHFFFAOYSA-N hexan-1-ol Chemical compound CCCCCCO ZSIAUFGUXNUGDI-UHFFFAOYSA-N 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 229910001092 metal group alloy Inorganic materials 0.000 description 2
- 229910000480 nickel oxide Inorganic materials 0.000 description 2
- GNRSAWUEBMWBQH-UHFFFAOYSA-N oxonickel Chemical compound [Ni]=O GNRSAWUEBMWBQH-UHFFFAOYSA-N 0.000 description 2
- 230000001737 promoting effect Effects 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 229910052723 transition metal Inorganic materials 0.000 description 2
- 150000003624 transition metals Chemical class 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- QGZKDVFQNNGYKY-UHFFFAOYSA-O Ammonium Chemical compound [NH4+] QGZKDVFQNNGYKY-UHFFFAOYSA-O 0.000 description 1
- VHUUQVKOLVNVRT-UHFFFAOYSA-N Ammonium hydroxide Chemical compound [NH4+].[OH-] VHUUQVKOLVNVRT-UHFFFAOYSA-N 0.000 description 1
- 229910002518 CoFe2O4 Inorganic materials 0.000 description 1
- 229910020515 Co—W Inorganic materials 0.000 description 1
- MYMOFIZGZYHOMD-UHFFFAOYSA-N Dioxygen Chemical compound O=O MYMOFIZGZYHOMD-UHFFFAOYSA-N 0.000 description 1
- 229910002549 Fe–Cu Inorganic materials 0.000 description 1
- 229910018487 Ni—Cr Inorganic materials 0.000 description 1
- 239000004372 Polyvinyl alcohol Substances 0.000 description 1
- 229920002125 Sokalan® Polymers 0.000 description 1
- 229910001080 W alloy Inorganic materials 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical compound [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- 235000011114 ammonium hydroxide Nutrition 0.000 description 1
- 230000008901 benefit Effects 0.000 description 1
- KGBXLFKZBHKPEV-UHFFFAOYSA-N boric acid Chemical compound OB(O)O KGBXLFKZBHKPEV-UHFFFAOYSA-N 0.000 description 1
- 239000003575 carbonaceous material Substances 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- VNNRSPGTAMTISX-UHFFFAOYSA-N chromium nickel Chemical compound [Cr].[Ni] VNNRSPGTAMTISX-UHFFFAOYSA-N 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- JPNWDVUTVSTKMV-UHFFFAOYSA-N cobalt tungsten Chemical compound [Co].[W] JPNWDVUTVSTKMV-UHFFFAOYSA-N 0.000 description 1
- 239000000571 coke Substances 0.000 description 1
- 239000000084 colloidal system Substances 0.000 description 1
- GOECOOJIPSGIIV-UHFFFAOYSA-N copper iron nickel Chemical compound [Fe].[Ni].[Cu] GOECOOJIPSGIIV-UHFFFAOYSA-N 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 230000018109 developmental process Effects 0.000 description 1
- 238000007598 dipping method Methods 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 239000010411 electrocatalyst Substances 0.000 description 1
- 239000011262 electrochemically active material Substances 0.000 description 1
- 239000002659 electrodeposit Substances 0.000 description 1
- 230000005288 electromagnetic effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000012530 fluid Substances 0.000 description 1
- 239000001866 hydroxypropyl methyl cellulose Substances 0.000 description 1
- 229920003088 hydroxypropyl methyl cellulose Polymers 0.000 description 1
- 235000010979 hydroxypropyl methyl cellulose Nutrition 0.000 description 1
- UFVKGYZPFZQRLF-UHFFFAOYSA-N hydroxypropyl methyl cellulose Chemical compound OC1C(O)C(OC)OC(CO)C1OC1C(O)C(O)C(OC2C(C(O)C(OC3C(C(O)C(O)C(CO)O3)O)C(CO)O2)O)C(CO)O1 UFVKGYZPFZQRLF-UHFFFAOYSA-N 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 235000014413 iron hydroxide Nutrition 0.000 description 1
- UGKDIUIOSMUOAW-UHFFFAOYSA-N iron nickel Chemical compound [Fe].[Ni] UGKDIUIOSMUOAW-UHFFFAOYSA-N 0.000 description 1
- NCNCGGDMXMBVIA-UHFFFAOYSA-L iron(ii) hydroxide Chemical compound [OH-].[OH-].[Fe+2] NCNCGGDMXMBVIA-UHFFFAOYSA-L 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- 229910044991 metal oxide Inorganic materials 0.000 description 1
- 150000004706 metal oxides Chemical class 0.000 description 1
- MOWMLACGTDMJRV-UHFFFAOYSA-N nickel tungsten Chemical compound [Ni].[W] MOWMLACGTDMJRV-UHFFFAOYSA-N 0.000 description 1
- QGLKJKCYBOYXKC-UHFFFAOYSA-N nonaoxidotritungsten Chemical compound O=[W]1(=O)O[W](=O)(=O)O[W](=O)(=O)O1 QGLKJKCYBOYXKC-UHFFFAOYSA-N 0.000 description 1
- 238000006213 oxygenation reaction Methods 0.000 description 1
- 238000010422 painting Methods 0.000 description 1
- 230000002093 peripheral effect Effects 0.000 description 1
- 238000007750 plasma spraying Methods 0.000 description 1
- 239000004584 polyacrylic acid Substances 0.000 description 1
- 229920000193 polymethacrylate Polymers 0.000 description 1
- 239000011118 polyvinyl acetate Substances 0.000 description 1
- 229920002689 polyvinyl acetate Polymers 0.000 description 1
- 229920002451 polyvinyl alcohol Polymers 0.000 description 1
- 239000011253 protective coating Substances 0.000 description 1
- 239000002994 raw material Substances 0.000 description 1
- 230000002787 reinforcement Effects 0.000 description 1
- 238000005245 sintering Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010409 thin film Substances 0.000 description 1
- 229910001930 tungsten oxide Inorganic materials 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25C—PROCESSES FOR THE ELECTROLYTIC PRODUCTION, RECOVERY OR REFINING OF METALS; APPARATUS THEREFOR
- C25C3/00—Electrolytic production, recovery or refining of metals by electrolysis of melts
- C25C3/06—Electrolytic production, recovery or refining of metals by electrolysis of melts of aluminium
- C25C3/08—Cell construction, e.g. bottoms, walls, cathodes
- C25C3/12—Anodes
-
- C—CHEMISTRY; METALLURGY
- C25—ELECTROLYTIC OR ELECTROPHORETIC PROCESSES; APPARATUS THEREFOR
- C25C—PROCESSES FOR THE ELECTROLYTIC PRODUCTION, RECOVERY OR REFINING OF METALS; APPARATUS THEREFOR
- C25C3/00—Electrolytic production, recovery or refining of metals by electrolysis of melts
- C25C3/06—Electrolytic production, recovery or refining of metals by electrolysis of melts of aluminium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Electrochemistry (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Electrolytic Production Of Metals (AREA)
- Battery Electrode And Active Subsutance (AREA)
- Electrodes For Compound Or Non-Metal Manufacture (AREA)
Abstract
A cell for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte, comprises a non-carbon metal-based anode having an electrically conductive metallic structure. This anode structure comprises an outer part with an electrochemically active anode surface on which, during electrolysis, oxygen is anodically evolved, and which is suspended in the electrolyte substantially parallel to a facing cathode.
The anode structure has one or more flow-through openings extending from the active anode surface through the metallic structure, the flow-through opening(s) being arranged for guiding a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises a layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode.
The anode structure has one or more flow-through openings extending from the active anode surface through the metallic structure, the flow-through opening(s) being arranged for guiding a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises a layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode.
Description
HIGH STABILITY FLOW-THROUGH NON-CARBON ANODES
FOR ALUMINIUM ELECTROWINNING
Field of the Invention This invention relates to the use in a molten electrolyte for the electrowinning of aluminium of a non-carbon anode having a flow-through active structure with an enhanced stability.
Background Art Using non-carbon anodes - i.e. anodes which are not made of carbon as such, e.g. graphite, coke, etc..., but possibly contain carbon in a compound - for the production of aluminium in electrolytic cells should drastically improve the aluminium production process by reducing pollution and the cost of aluminium production.
The developments of non-carbon anode materials, in particular metals, led to the design of new anode shapes that are better adapted to the cell's fluid mechanisms and electromagnetic effects than the conventional anodic solid carbon blocks.
Several designs for oxygen-evolving anodes for aluminium electrowinning cells were proposed in the following documents. US Patent 4,681,671 (Duruz) discloses vertical anode plates or blades operated in low temperature aluminium electrowinning cells. US Patent 5,310,476 (Sekhar/de Nora) discloses oxygen-evolving anodes consisting of roof-like assembled pairs of anode plates. US Patent 5,362,366 (de Nora/Sekhar) describes non-consumable anode shapes including roof-like assembled pairs of anode plates. US Patent 5,368,702 (de Nora) discloses vertical tubular or frustoconical oxygen-evolving anodes for multimonopolar aluminium cells. US
Patent 5,683,559 (de Nora) describes an aluminium electrowinning cell with oxygen-evolving bent anode plates which are aligned in a roof-like configuration facing correspondingly shaped cathodes. US Patent 5,725,744 (de Nora/Duruz) discloses vertical oxygen-evolving anode plates, preferably porous or reticulated,
FOR ALUMINIUM ELECTROWINNING
Field of the Invention This invention relates to the use in a molten electrolyte for the electrowinning of aluminium of a non-carbon anode having a flow-through active structure with an enhanced stability.
Background Art Using non-carbon anodes - i.e. anodes which are not made of carbon as such, e.g. graphite, coke, etc..., but possibly contain carbon in a compound - for the production of aluminium in electrolytic cells should drastically improve the aluminium production process by reducing pollution and the cost of aluminium production.
The developments of non-carbon anode materials, in particular metals, led to the design of new anode shapes that are better adapted to the cell's fluid mechanisms and electromagnetic effects than the conventional anodic solid carbon blocks.
Several designs for oxygen-evolving anodes for aluminium electrowinning cells were proposed in the following documents. US Patent 4,681,671 (Duruz) discloses vertical anode plates or blades operated in low temperature aluminium electrowinning cells. US Patent 5,310,476 (Sekhar/de Nora) discloses oxygen-evolving anodes consisting of roof-like assembled pairs of anode plates. US Patent 5,362,366 (de Nora/Sekhar) describes non-consumable anode shapes including roof-like assembled pairs of anode plates. US Patent 5,368,702 (de Nora) discloses vertical tubular or frustoconical oxygen-evolving anodes for multimonopolar aluminium cells. US
Patent 5,683,559 (de Nora) describes an aluminium electrowinning cell with oxygen-evolving bent anode plates which are aligned in a roof-like configuration facing correspondingly shaped cathodes. US Patent 5,725,744 (de Nora/Duruz) discloses vertical oxygen-evolving anode plates, preferably porous or reticulated,
2 -in a multimonopolar cell arrangement for aluminium electrowinning cells operating at reduced temperature.
W000/40781, W000/40782 and W003/006716 (all de Nora) both disclose aluminium production anodes with a series of parallel spaced-apart elongated anode members which are electrochemically active for the oxidation of oxygen.
For the dissolution of the raw material alumina, a highly aggressive fluoride-based electrolyte, such as cryolite, is required. Various modified electrolytes have been proposed to improve cell operation and reduce wear of non-carbon metal-based anode, particularly caused by corrosion by the electrolyte.
W000/06804 (Crottaz/Duruz) teaches that a nickel-iron anode can be used in an electrolyte at a temperature of 8200 to 870 C containing 23 to 26.5 weight% A1F3, 3 to 5 weight% A1203, 1 to 2 weight% LiF and 1 to 2 weighto MgF2. US Patents 5,006,209 and 5,284,562 (both Beck/Brooks), 6,258,247 and 6,379,512 (both Brown/
Brooks/Frizzle/Juric), 6,419,813 (Brown/Brooks/Frizzle) and 6,436,272 (Brown/Frizzle) all disclose the use of nickel-copper-iron anodes in an aluminium production electrolyte at 660 -800 C containing 6-26 weight% NaF, 7-33 weight% KF, 1-6 weight% LiF and 60-65 weight% AlF3.
The electrolyte may contain A1203 in an amount of up to 30 weight%, in particular 5 to 10 or 15 weight%, most of which is in the form of suspended particles and some of which is dissolved in the electrolyte, i.e. typically 1 to 4 weighto dissolved A1203. In US Patents 6,258,247, 6,379,512, 6,419,813 and 6,436,272 such an electrolyte is said to be useable at temperatures up to 900 C. In US
Patents 6,258,247 and 6,379,512 the electrolyte further contains 0.004 to 0.2 weight% transition metal additives to facilitate alumina dissolution and improve cathodic operation. US Patent 5,725,744 (de Nora/Duruz) discloses an aluminium production cell having anodes made of nickel, iron and/or copper in a electrolyte at a temperature from 680 to 880 C containing 42-63 weight%
AlF3, up to 48 weight% NaF, up to 48 weight% LiF and 1 to 5 weight o A1203. MgF2, KF and CaF2 are also mentioned as possible bath constituents. W02004/035871 (de Nora/Nguyen/Duruz) discloses a metal-based anode
W000/40781, W000/40782 and W003/006716 (all de Nora) both disclose aluminium production anodes with a series of parallel spaced-apart elongated anode members which are electrochemically active for the oxidation of oxygen.
For the dissolution of the raw material alumina, a highly aggressive fluoride-based electrolyte, such as cryolite, is required. Various modified electrolytes have been proposed to improve cell operation and reduce wear of non-carbon metal-based anode, particularly caused by corrosion by the electrolyte.
W000/06804 (Crottaz/Duruz) teaches that a nickel-iron anode can be used in an electrolyte at a temperature of 8200 to 870 C containing 23 to 26.5 weight% A1F3, 3 to 5 weight% A1203, 1 to 2 weight% LiF and 1 to 2 weighto MgF2. US Patents 5,006,209 and 5,284,562 (both Beck/Brooks), 6,258,247 and 6,379,512 (both Brown/
Brooks/Frizzle/Juric), 6,419,813 (Brown/Brooks/Frizzle) and 6,436,272 (Brown/Frizzle) all disclose the use of nickel-copper-iron anodes in an aluminium production electrolyte at 660 -800 C containing 6-26 weight% NaF, 7-33 weight% KF, 1-6 weight% LiF and 60-65 weight% AlF3.
The electrolyte may contain A1203 in an amount of up to 30 weight%, in particular 5 to 10 or 15 weight%, most of which is in the form of suspended particles and some of which is dissolved in the electrolyte, i.e. typically 1 to 4 weighto dissolved A1203. In US Patents 6,258,247, 6,379,512, 6,419,813 and 6,436,272 such an electrolyte is said to be useable at temperatures up to 900 C. In US
Patents 6,258,247 and 6,379,512 the electrolyte further contains 0.004 to 0.2 weight% transition metal additives to facilitate alumina dissolution and improve cathodic operation. US Patent 5,725,744 (de Nora/Duruz) discloses an aluminium production cell having anodes made of nickel, iron and/or copper in a electrolyte at a temperature from 680 to 880 C containing 42-63 weight%
AlF3, up to 48 weight% NaF, up to 48 weight% LiF and 1 to 5 weight o A1203. MgF2, KF and CaF2 are also mentioned as possible bath constituents. W02004/035871 (de Nora/Nguyen/Duruz) discloses a metal-based anode
3 -containing at least one of nickel, cobalt and iron. The anode is used for electrowinning aluminium in a fluoride-containing molten electrolyte consisting of: 5 to 14 wt%
dissolved alumina; 35 to 45 wt% aluminium fluoride; 30 to 45 wt% sodium fluoride; 5 to 20 wt% potassium fluoride; 0 to 5 wt% calcium fluoride; and 0 to 5 wt% of further constituents.
The materials having the greatest resistance to oxidation are metal oxides which are all to some extent soluble in cryolite. Oxides are also poorly electrically conductive, therefore, to avoid substantial ohmic losses and high cell voltages, the use of non-conductive or poorly conductive oxides should be minimal in the manufacture of anodes. Whenever possible, a good conductive material should be utilised for the anode core, whereas the surface of the anode is preferably made of an oxide having a high electrocatalytic activity.
Several attempts have been made in order to develop non-carbon anodes for aluminium electrowinning cells, resistant to chemical attacks of the bath and by the cell environment, and with an electrochemical active surface for the oxidation of oxygen ions to atomic and molecular gaseous oxygen and having a low dissolution rate. Many patents have been filed on non-carbon anodes but none has found commercial acceptance yet, also because of economical reasons.
US Patent 4,614,569 (Duruz/Derivaz/Debely/Adorian) describes metal anodes for aluminium electrowinning coated with a protective coating of cerium oxyfluoride, formed in-situ in the cell or pre-applied, this coating being maintained during electrolysis by the addition of small amounts of a cerium compound to the molten cryolite electrolyte so as to protect the surface of the anode from the electrolyte attack. Several patents disclose the use of an electrically conductive metal anode core with an oxide-based active outer part, in particular US
patents 4,956,069, 4,960,494, 5,069,771 (all Nguyen/Lazouni/Doan), 6,077,415 (Duruz/de Nora), 6,103,090 (de Nora), 6,113,758 (de Nora/Duruz) and 6,248,227 (de Nora/Duruz), 6,361,681 (de Nora/Duruz), 6,365,018 (de Nora), 6,372,099 (Duruz/de Nora), 6,379,526
dissolved alumina; 35 to 45 wt% aluminium fluoride; 30 to 45 wt% sodium fluoride; 5 to 20 wt% potassium fluoride; 0 to 5 wt% calcium fluoride; and 0 to 5 wt% of further constituents.
The materials having the greatest resistance to oxidation are metal oxides which are all to some extent soluble in cryolite. Oxides are also poorly electrically conductive, therefore, to avoid substantial ohmic losses and high cell voltages, the use of non-conductive or poorly conductive oxides should be minimal in the manufacture of anodes. Whenever possible, a good conductive material should be utilised for the anode core, whereas the surface of the anode is preferably made of an oxide having a high electrocatalytic activity.
Several attempts have been made in order to develop non-carbon anodes for aluminium electrowinning cells, resistant to chemical attacks of the bath and by the cell environment, and with an electrochemical active surface for the oxidation of oxygen ions to atomic and molecular gaseous oxygen and having a low dissolution rate. Many patents have been filed on non-carbon anodes but none has found commercial acceptance yet, also because of economical reasons.
US Patent 4,614,569 (Duruz/Derivaz/Debely/Adorian) describes metal anodes for aluminium electrowinning coated with a protective coating of cerium oxyfluoride, formed in-situ in the cell or pre-applied, this coating being maintained during electrolysis by the addition of small amounts of a cerium compound to the molten cryolite electrolyte so as to protect the surface of the anode from the electrolyte attack. Several patents disclose the use of an electrically conductive metal anode core with an oxide-based active outer part, in particular US
patents 4,956,069, 4,960,494, 5,069,771 (all Nguyen/Lazouni/Doan), 6,077,415 (Duruz/de Nora), 6,103,090 (de Nora), 6,113,758 (de Nora/Duruz) and 6,248,227 (de Nora/Duruz), 6,361,681 (de Nora/Duruz), 6,365,018 (de Nora), 6,372,099 (Duruz/de Nora), 6,379,526
4 -(Duruz/de Nora), 6,413,406 (de Nora), 6,425,992 (de Nora), 6,436,274 (de Nora/Duruz), 6,521,116 (Duruz/de Nora/Crottaz), 6,521,115 (Duruz/de Nora/Crottaz), 6,533,909 (Duruz/de Nora), 6,562,224 (Crottaz/Duruz) as well as PCT publications W000/40783 (de Nora/Duruz), WO01/42534 (de Nora/Duruz), W001/42535 (Duruz/de Nora), WO01/42536 (Nguyen/Duruz/ de Nora), W002/070786 (Nguyen/de Nora), W002/083990 (de Nora/Nguyen), W002/083991 (Nguyen/de Nora), W003/014420 (Nguyen/Duruz/de Nora), W003/078695(Nguyen/de Nora), W003/087435 (Nguyen/de Nora).
US 4,374,050 (Ray) discloses numerous multiple oxide compositions for electrodes. Such compositions inter-alia include oxides of iron and cobalt. The oxide compositions can be used as a cladding on a metal layer of nickel, nickel-chromium, steel, copper, cobalt or molybdenum. US
4,142,005 (Cadwell/Hazelrigg) discloses an anode having a substrate made of titanium, tantalum, tungsten, zirconium, molybdenum, niobium, hafnium or vanadium. The substrate is coated with cobalt oxide Co304.
US 6,103,090 (de Nora), 6,361,681 (de Nora/Duruz), 6,365,018 (de Nora), 6,379,526 (de Nora/Duruz), 6,413,406 (de Nora) and 6,425,992 (de Nora), and W004/018731 (Nguyen/de Nora) disclose anode substrates that contain at least one of chromium, cobalt, hafnium, iron, molybdenum, nickel, copper, niobium, platinum, silicon, tantalum, titanium, tungsten, vanadium, yttrium and zirconium and that are coated with at least one of ferrites of cobalt, copper, chromium, manganese, nickel and zinc. WO01/42535 (Duruz/de Nora) and W002/097167 (Nguyen/de Nora), disclose aluminium electrowinning anodes made of surface oxidised iron alloys that contain at least one of nickel and cobalt. US 6,638,412 (de Nora/Duruz) discloses the use of anodes made of a transition metal-containing alloy having an integral oxide layer, the alloy comprising at least one of iron, nickel and cobalt.
Non-carbon anodes have not as yet been commercially and industrially applied and there is still a need for a metal-based anodic material and an appropriate anode shape that can be used for electrowinning aluminium.
-Summary of the Invention The present invention generally relates to aluminium electrowinning with metal-based anodes having a shape for promoting an electrolyte circulation and having an
US 4,374,050 (Ray) discloses numerous multiple oxide compositions for electrodes. Such compositions inter-alia include oxides of iron and cobalt. The oxide compositions can be used as a cladding on a metal layer of nickel, nickel-chromium, steel, copper, cobalt or molybdenum. US
4,142,005 (Cadwell/Hazelrigg) discloses an anode having a substrate made of titanium, tantalum, tungsten, zirconium, molybdenum, niobium, hafnium or vanadium. The substrate is coated with cobalt oxide Co304.
US 6,103,090 (de Nora), 6,361,681 (de Nora/Duruz), 6,365,018 (de Nora), 6,379,526 (de Nora/Duruz), 6,413,406 (de Nora) and 6,425,992 (de Nora), and W004/018731 (Nguyen/de Nora) disclose anode substrates that contain at least one of chromium, cobalt, hafnium, iron, molybdenum, nickel, copper, niobium, platinum, silicon, tantalum, titanium, tungsten, vanadium, yttrium and zirconium and that are coated with at least one of ferrites of cobalt, copper, chromium, manganese, nickel and zinc. WO01/42535 (Duruz/de Nora) and W002/097167 (Nguyen/de Nora), disclose aluminium electrowinning anodes made of surface oxidised iron alloys that contain at least one of nickel and cobalt. US 6,638,412 (de Nora/Duruz) discloses the use of anodes made of a transition metal-containing alloy having an integral oxide layer, the alloy comprising at least one of iron, nickel and cobalt.
Non-carbon anodes have not as yet been commercially and industrially applied and there is still a need for a metal-based anodic material and an appropriate anode shape that can be used for electrowinning aluminium.
-Summary of the Invention The present invention generally relates to aluminium electrowinning with metal-based anodes having a shape for promoting an electrolyte circulation and having an
5 electrochemically active outer part that has an enhanced stability against corrosion by the highly aggressive circulating electrolyte and/or against oxidation by anodically evolved oxygen, the enhanced stability being provided by a layer that contains predominantly cobalt oxide CoO.
In particular, the invention relates to a cell for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte. The cell comprises at least one non-carbon metal-based anode having an electrically conductive metallic structure that comprises an outer part with an electrochemically active anode surface on which, during electrolysis, oxygen is anodically evolved, and which is suspended in the electrolyte substantially parallel to a facing cathode.
This metallic structure has one or more flow-through openings extending from the active anode surface through the metallic structure, the flow-through opening(s) being arranged for guiding a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises the abovementioned layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode.
In other words, the invention concerns a cell having an anode that has a shape that promotes electrolyte circulation and that has an electrochemically active outer part that is resistant to the circulating electrolyte and/or to anodically evolved oxygen by the presence of a layer made predominantly of a special form of cobalt oxide, i.e. CoO.
There are several forms of stoichiometric and non-stoichiometric cobalt oxides which are based on:
- CoO that contains Co(II) and that is formed predominantly at a temperature above 920 C in air;
In particular, the invention relates to a cell for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte. The cell comprises at least one non-carbon metal-based anode having an electrically conductive metallic structure that comprises an outer part with an electrochemically active anode surface on which, during electrolysis, oxygen is anodically evolved, and which is suspended in the electrolyte substantially parallel to a facing cathode.
This metallic structure has one or more flow-through openings extending from the active anode surface through the metallic structure, the flow-through opening(s) being arranged for guiding a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises the abovementioned layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode.
In other words, the invention concerns a cell having an anode that has a shape that promotes electrolyte circulation and that has an electrochemically active outer part that is resistant to the circulating electrolyte and/or to anodically evolved oxygen by the presence of a layer made predominantly of a special form of cobalt oxide, i.e. CoO.
There are several forms of stoichiometric and non-stoichiometric cobalt oxides which are based on:
- CoO that contains Co(II) and that is formed predominantly at a temperature above 920 C in air;
6 PCT/IB2005/051718 - Co203 that contains Co(III) and that is formed at temperatures up to 895 C and at higher temperatures begins to decompose into CoO;
- Co3O4 that contains Co(II) and Co(III) and that is formed at temperatures between 300 and 900 C.
It has been observed that - unlike Co203 that is unstable and Co304 that does not significantly inhibit oxygen diffusion - CoO forms a well conductive electrochemically active material for the oxidation of oxygen ions and for inhibiting diffusion of oxygen. Thus this material forms a limited barrier against oxidation of the metallic cobalt body underneath.
The anode's CoO-containing layer can be a layer made of sintered particles, especially sintered CoO particles.
15' Alternatively, the Co0-containing layer may be an integral oxide layer on a Co-containing metallic layer or anode core. Tests have shown that integral oxide layers have a higher density than sintered layers and are thus preferred to inhibit oxygen diffusion.
When CoO is to be formed by oxidising metallic cobalt, care should be taken to carry out a treatment that will indeed result in the formation of CoO. It was found that using Co2O3 or Co3O4 in a known aluminium electrowinning electrolyte does not lead to an appropriate conversion of these forms of cobalt oxide into CoO. Therefore, it is important to provide an anode with the CoO layer before the anode is used in an aluminium electrowinning electrolyte.
The formation of CoO on the metallic cobalt is preferably controlled so as to produce a coherent and substantially crack-free oxide layer. However, not any treatment of metallic cobalt at a temperature above 895 C
or 900 C in an oxygen-containing atmosphere will result in optimal coherent and substantially crack-free CoO
layer that offers better electrochemical properties than a C02O3/CO3O4.
For instance, if the temperature for treating the metallic cobalt to form Co0 by air oxidation of metallic
- Co3O4 that contains Co(II) and Co(III) and that is formed at temperatures between 300 and 900 C.
It has been observed that - unlike Co203 that is unstable and Co304 that does not significantly inhibit oxygen diffusion - CoO forms a well conductive electrochemically active material for the oxidation of oxygen ions and for inhibiting diffusion of oxygen. Thus this material forms a limited barrier against oxidation of the metallic cobalt body underneath.
The anode's CoO-containing layer can be a layer made of sintered particles, especially sintered CoO particles.
15' Alternatively, the Co0-containing layer may be an integral oxide layer on a Co-containing metallic layer or anode core. Tests have shown that integral oxide layers have a higher density than sintered layers and are thus preferred to inhibit oxygen diffusion.
When CoO is to be formed by oxidising metallic cobalt, care should be taken to carry out a treatment that will indeed result in the formation of CoO. It was found that using Co2O3 or Co3O4 in a known aluminium electrowinning electrolyte does not lead to an appropriate conversion of these forms of cobalt oxide into CoO. Therefore, it is important to provide an anode with the CoO layer before the anode is used in an aluminium electrowinning electrolyte.
The formation of CoO on the metallic cobalt is preferably controlled so as to produce a coherent and substantially crack-free oxide layer. However, not any treatment of metallic cobalt at a temperature above 895 C
or 900 C in an oxygen-containing atmosphere will result in optimal coherent and substantially crack-free CoO
layer that offers better electrochemical properties than a C02O3/CO3O4.
For instance, if the temperature for treating the metallic cobalt to form Co0 by air oxidation of metallic
7 -cobalt is increased at an insufficient rate, e.g. less than 200 C/hour, a thick oxide layer rich in Co304 and in glassy Coz03 is formed at the surface of the metallic cobalt. Such a layer does not permit optimal formation of the CoO layer by conversion at a temperature above 895 C
of Co203 and Co304 into CoO. In fact, a layer of CoO
resulting from such conversion is not preferred but still useful despite an increased porosity and may be cracked.
Therefore, the required temperature for air oxidation, i.e. above 900 C, usually at least 920 C or preferably above 940 C should be attained sufficiently quickly, e.g.
at a rate of increase of the temperature of at least 300 C or 600 C per hour to obtain an optimal CoO layer.
The metallic cobalt may also be placed into an oven that is pre-heated at the desired temperature above 900 C.
Likewise, if the anode is not immediately used for the electrowinning of aluminium after formation of the CoO layer but allowed to cool down, the cooling down should be carried out sufficiently fast, for example by placing the anode in air at room temperature, to avoid significant formation of Co304 that could occur during the cooling, for instance in an oven that is switched off.
An anode with a CoO layer obtained by slow heating of the metallic cobalt in an oxidising environment will not have optimal properties but still provides better results during cell operation than an anode having a COZO3-CO3O4 layer and therefore also constitutes an improved aluminium electrowinning anode according to the invention.
The anode structure can be foraminate. For instance, the anode structure can have any of the shapes disclosed in the abovementioned W000/40781, W000/40782 and WO03/006716. For example, the anode structure comprises a series of parallel anode members, in particular horizontal anode members having electrochemically active surfaces in a generally coplanar arrangement to form said active anode surface, the anode members being spaced apart to form longitudinal flow-through openings for the circulation of electrolyte driven by the fast escape of anodically evolved oxygen. Typically these anode members
of Co203 and Co304 into CoO. In fact, a layer of CoO
resulting from such conversion is not preferred but still useful despite an increased porosity and may be cracked.
Therefore, the required temperature for air oxidation, i.e. above 900 C, usually at least 920 C or preferably above 940 C should be attained sufficiently quickly, e.g.
at a rate of increase of the temperature of at least 300 C or 600 C per hour to obtain an optimal CoO layer.
The metallic cobalt may also be placed into an oven that is pre-heated at the desired temperature above 900 C.
Likewise, if the anode is not immediately used for the electrowinning of aluminium after formation of the CoO layer but allowed to cool down, the cooling down should be carried out sufficiently fast, for example by placing the anode in air at room temperature, to avoid significant formation of Co304 that could occur during the cooling, for instance in an oven that is switched off.
An anode with a CoO layer obtained by slow heating of the metallic cobalt in an oxidising environment will not have optimal properties but still provides better results during cell operation than an anode having a COZO3-CO3O4 layer and therefore also constitutes an improved aluminium electrowinning anode according to the invention.
The anode structure can be foraminate. For instance, the anode structure can have any of the shapes disclosed in the abovementioned W000/40781, W000/40782 and WO03/006716. For example, the anode structure comprises a series of parallel anode members, in particular horizontal anode members having electrochemically active surfaces in a generally coplanar arrangement to form said active anode surface, the anode members being spaced apart to form longitudinal flow-through openings for the circulation of electrolyte driven by the fast escape of anodically evolved oxygen. Typically these anode members
8 -are blades, bars, rods or wires. The active anode surface can be substantially horizontal, substantially vertical or inclined to the horizontal, for example as disclosed in W000/40782 or W003/023092 (both de Nora).
In one embodiment, the molten electrolyte is at a temperature below 950 C, in particular in the range from 9100 to 940 C, and consists of:
- 6.5 to 11 weight% dissolved alumina, in particular 7 to 10 weighto;
- 35 to 44 weight s aluminium fluoride, in particular 36 to 42 weight% aluminium fluoride, such as 36 to 38 weight;
- 38 to 46 weight% sodium fluoride, in particular 39 to 43 weight%;
- 2 to 15 weight% potassium fluoride, in particular 3 to 10 weight% potassium fluoride, such as 5 to 7 weight%;
- 0 to 5 weight% calcium fluoride, in particular 2 to 4 weight% calcium fluoride; and - 0 to 5 weight% in total of one or more further constituents, in particular up to 3 weight%.
The presence in the electrolyte of potassium fluoride in the above amount has two effects. On the one hand, it leads to a reduction of the operating temperature by up to several tens of degrees without increase of the electrolyte's aluminium fluoride content or even a reduction thereof compared to standard electrolytes operating at about 950 C with an aluminium fluoride content of about 45 weight%. On the other hand, it maintains a high solubility of alumina, i.e. up to above about 8 or 9 weighto, in the electrolyte even though the temperature of the electrolyte is reduced compared to conventional temperature.
Hence, in contrast to prior art low temperature electrolytes which carry large amounts of undissolved alumina in particulate form, a large amount of alumina is in a dissolved form in the above electrolyte.
Without being bound to any theory, it is believed that combining a high concentration of dissolved alumina in the electrolyte and a limited concentration of aluminium fluoride leads predominantly to the formation
In one embodiment, the molten electrolyte is at a temperature below 950 C, in particular in the range from 9100 to 940 C, and consists of:
- 6.5 to 11 weight% dissolved alumina, in particular 7 to 10 weighto;
- 35 to 44 weight s aluminium fluoride, in particular 36 to 42 weight% aluminium fluoride, such as 36 to 38 weight;
- 38 to 46 weight% sodium fluoride, in particular 39 to 43 weight%;
- 2 to 15 weight% potassium fluoride, in particular 3 to 10 weight% potassium fluoride, such as 5 to 7 weight%;
- 0 to 5 weight% calcium fluoride, in particular 2 to 4 weight% calcium fluoride; and - 0 to 5 weight% in total of one or more further constituents, in particular up to 3 weight%.
The presence in the electrolyte of potassium fluoride in the above amount has two effects. On the one hand, it leads to a reduction of the operating temperature by up to several tens of degrees without increase of the electrolyte's aluminium fluoride content or even a reduction thereof compared to standard electrolytes operating at about 950 C with an aluminium fluoride content of about 45 weight%. On the other hand, it maintains a high solubility of alumina, i.e. up to above about 8 or 9 weighto, in the electrolyte even though the temperature of the electrolyte is reduced compared to conventional temperature.
Hence, in contrast to prior art low temperature electrolytes which carry large amounts of undissolved alumina in particulate form, a large amount of alumina is in a dissolved form in the above electrolyte.
Without being bound to any theory, it is believed that combining a high concentration of dissolved alumina in the electrolyte and a limited concentration of aluminium fluoride leads predominantly to the formation
9 -of (basic) fluorine-poor aluminium oxyfluoride ions ([A1202F4] 2-) instead of (acid) fluorine-rich aluminium oxyfluoride ions ([A120F6]2-) near the anode. As opposed to acid fluorine-rich aluminium oxyfluoride ions, basic fluorine-poor aluminium oxyfluoride ions do not significantly dissolve the anode's CoO and do not noticeably passivate or corrode metallic cobalt. The weight ratio of dissolved alumina/aluminium fluoride in the electrolyte should be above 1/7, and often above 1/6 or even above 1/5, to obtain a favourable ratio of the fluorine-poor aluminium oxyfluoride ions and the fluorine-rich aluminium oxyfluoride ions.
It follows that the use of the above described electrolyte with metal-based anodes that contains CoO
inhibits its dissolution, passivation and corrosion.
Moreover, a high concentration of alumina dissolved in the electrolyte further reduces dissolution of oxides of the anode, in particular CoO.
The electrolyte may consist of: 7 to 10 weight%
dissolved alumina; 36 to 42 weight% aluminium fluoride, in particular 36 to 38 weight%; 39 to 43 weight% sodium fluoride; 3 to 10 weight% potassium fluoride, such as 5 to 7 weight%; 2 to 4 weight% calcium fluoride; and 0 to 3 weight% in total of one or more further constituents.
This corresponds to a cryolite-based (Na3AlF6) molten electrolyte containing an excess of aluminium fluoride (AlF3) that is in the range of about 8 to 15 weight% of the electrolyte, in particular about 8 to 10 weight%, and additives that can include potassium fluoride and calcium fluoride in the abovementioned amounts.
The electrolyte can contain as further constituent(s) at least one fluoride selected from magnesium fluoride, lithium fluoride, cesium fluoride, rubidium fluoride, strontium fluoride, barium fluoride and cerium fluoride.
Advantageously, The electrolyte contains alumina at a concentration near saturation on the active anode surface.
It follows that the use of the above described electrolyte with metal-based anodes that contains CoO
inhibits its dissolution, passivation and corrosion.
Moreover, a high concentration of alumina dissolved in the electrolyte further reduces dissolution of oxides of the anode, in particular CoO.
The electrolyte may consist of: 7 to 10 weight%
dissolved alumina; 36 to 42 weight% aluminium fluoride, in particular 36 to 38 weight%; 39 to 43 weight% sodium fluoride; 3 to 10 weight% potassium fluoride, such as 5 to 7 weight%; 2 to 4 weight% calcium fluoride; and 0 to 3 weight% in total of one or more further constituents.
This corresponds to a cryolite-based (Na3AlF6) molten electrolyte containing an excess of aluminium fluoride (AlF3) that is in the range of about 8 to 15 weight% of the electrolyte, in particular about 8 to 10 weight%, and additives that can include potassium fluoride and calcium fluoride in the abovementioned amounts.
The electrolyte can contain as further constituent(s) at least one fluoride selected from magnesium fluoride, lithium fluoride, cesium fluoride, rubidium fluoride, strontium fluoride, barium fluoride and cerium fluoride.
Advantageously, The electrolyte contains alumina at a concentration near saturation on the active anode surface.
- 10 -In order to maintain the alumina concentration above a given threshold in the abovementioned range during normal electrolysis, the cell is preferably fitted with means to monitor and adjust the electrolyte's alumina content.
The CoO-containing anode layer can be integral with a core made of cobalt or a cobalt alloy. Such an anode core can be made of the same materials as the Co-containing alloys described below. The cobalt-containing anode core can advantageously be cast.
Alternatively, the anode comprises an electrically conductive substrate that is covered with an applied electrochemically active coating that comprises the CoO-containing layer.
The Co0-containing layer can be a layer of sintered particles. In particular, the Co0-containing layer can be formed by applying a layer of particulate CoO to the anode and sintering. For instance, the Co0-containing layer is applied as a slurry, in particular a colloidal and/or polymeric slurry, and then heat treated. Good results have been obtained by slurring particulate metallic cobalt or CoO, optionally with additives such as Ta, in an acqueous solution containing at least one of ethylene glycol, hexanol, polyvinyl alcohol, polyvinyl acetate, polyacrylic acid, hydroxy propyl methyl cellulose and ammonium polymethacrylate and mixtures thereof, followed by application to the anode, e.g.
painting or dipping, and heat treating.
The Co0-containing layer can be an integral oxide layer on an applied Co-containing metallic layer of the coating.
The Co0-containing layer can be formed by applying a Co-containing metallic layer to the anode and subjecting the metallic layer to an oxidation treatment to form the CoO-containing layer on the metallic layer, the CoO-containing layer being integral with the metallic layer.
Conveniently, the oxidation treatment can be carried out in an oxygen containing atmosphere, such as air. The
The CoO-containing anode layer can be integral with a core made of cobalt or a cobalt alloy. Such an anode core can be made of the same materials as the Co-containing alloys described below. The cobalt-containing anode core can advantageously be cast.
Alternatively, the anode comprises an electrically conductive substrate that is covered with an applied electrochemically active coating that comprises the CoO-containing layer.
The Co0-containing layer can be a layer of sintered particles. In particular, the Co0-containing layer can be formed by applying a layer of particulate CoO to the anode and sintering. For instance, the Co0-containing layer is applied as a slurry, in particular a colloidal and/or polymeric slurry, and then heat treated. Good results have been obtained by slurring particulate metallic cobalt or CoO, optionally with additives such as Ta, in an acqueous solution containing at least one of ethylene glycol, hexanol, polyvinyl alcohol, polyvinyl acetate, polyacrylic acid, hydroxy propyl methyl cellulose and ammonium polymethacrylate and mixtures thereof, followed by application to the anode, e.g.
painting or dipping, and heat treating.
The Co0-containing layer can be an integral oxide layer on an applied Co-containing metallic layer of the coating.
The Co0-containing layer can be formed by applying a Co-containing metallic layer to the anode and subjecting the metallic layer to an oxidation treatment to form the CoO-containing layer on the metallic layer, the CoO-containing layer being integral with the metallic layer.
Conveniently, the oxidation treatment can be carried out in an oxygen containing atmosphere, such as air. The
- 11 -treatment can also be carried out in an atmosphere that is oxygen rich or consists essentially of pure oxygen.
It is also contemplated to carry out this oxidation treatment by other means, for instance electrolytically.
However, it was found that full formation of the CoO
integral layer cannot be achieved in-situ during aluminium electrowinning under normal cell operating conditions. In other words, when the anode is intended for use in a non-carbon anode aluminium electrowinning cell operating under the usual conditions, the anode should always be placed into the cell with a preformed integral oxide layer containing predominantly CoO.
As the conversion of Co(III) into Co(II) occurs at a temperature of about 895 C, the oxidation treatment should be carried out above this temperature. Usually, the oxidation treatment is carried out at a treatment temperature above 895 C or 920 C, preferably above 940 C, in particular within the range of 950 C to 1050 C. The Co-containing metallic layer can be heated from 'room temperature to this treatment temperature at a rate of at least 300 C/hour, in particular at least 450 C/hour, or is placed in an environment, in particular in an oven, that is preheated to said temperature. The oxidation treatment at this treatment temperature can be carried out for more than 8 or 12 hours, in particular from 16 to 48 hours. Especially when the oxygen-content of the oxidising atmosphere is increased, the duration of the treatment can be reduced below 8 hours, for example down to 4 hours.
The Co-containing metallic layer can be further oxidised during use. However, the main formation of CoO
is preferably achieved before use and in a controlled manner for the reasons explained above.
The method for forming the CoO-containing layer on the Co-containing metallic layer can be used to form the Co0-containing layer on the previously mentioned Co-containing anode core.
It is also contemplated to carry out this oxidation treatment by other means, for instance electrolytically.
However, it was found that full formation of the CoO
integral layer cannot be achieved in-situ during aluminium electrowinning under normal cell operating conditions. In other words, when the anode is intended for use in a non-carbon anode aluminium electrowinning cell operating under the usual conditions, the anode should always be placed into the cell with a preformed integral oxide layer containing predominantly CoO.
As the conversion of Co(III) into Co(II) occurs at a temperature of about 895 C, the oxidation treatment should be carried out above this temperature. Usually, the oxidation treatment is carried out at a treatment temperature above 895 C or 920 C, preferably above 940 C, in particular within the range of 950 C to 1050 C. The Co-containing metallic layer can be heated from 'room temperature to this treatment temperature at a rate of at least 300 C/hour, in particular at least 450 C/hour, or is placed in an environment, in particular in an oven, that is preheated to said temperature. The oxidation treatment at this treatment temperature can be carried out for more than 8 or 12 hours, in particular from 16 to 48 hours. Especially when the oxygen-content of the oxidising atmosphere is increased, the duration of the treatment can be reduced below 8 hours, for example down to 4 hours.
The Co-containing metallic layer can be further oxidised during use. However, the main formation of CoO
is preferably achieved before use and in a controlled manner for the reasons explained above.
The method for forming the CoO-containing layer on the Co-containing metallic layer can be used to form the Co0-containing layer on the previously mentioned Co-containing anode core.
- 12 -The Co-containing metallic layer can contain alloying metals for further reducing oxygen diffusion and/or corrosion through the metallic layer.
In one embodiment, the anode comprises an oxygen barrier layer between the CoO-containing layer and the electrically conductive substrate. The oxygen barrier layer can contain at least one metal selected from nickel, copper, tungsten, molybdenum, tantalum, niobium and chromium, or an oxide thereof, for example alloyed with cobalt, such as a cobalt alloy containing tungsten, molybdenum, tantalum and/or niobium, in particular an alloy containing: at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wto, such as 10 to 20 wt%; and one or more further elements and compounds in a total amount of up to 5 wt%
such as 0.01 to 4 weighto, the balance being cobalt.
These further elements may contain at least one of aluminium, silicon and manganese.
Typically, the oxygen barrier layer and the CoO-containing layer are formed by oxidising the surface of an applied layer of the abovementioned cobalt alloy that contains nickel, tungsten, molybdenum, tantalum and/or niobium. The resulting CoO-containing layer is predominantly made of CoO and is integral with the unoxidised part of the metallic cobalt alloy that forms the oxygen barrier layer.
When the CoO layer is integral with the cobalt alloy, the nickel, when present, should be contained in the alloy in an amount of up to 20 weight%, in particular 5 to 15 weight%. Such an amount of nickel in the alloy leads to the formation of a small amount of nickel oxide NiO in the integral oxide layer, in about the same proportions to cobalt as in the metallic part, i.e. 5 to 15 or 20 weight%. It has been observed that the presence of a small amount of nickel oxide stabilises the cobalt oxide CoO and durably inhibits the formation of Co2O3 or Co3O4. However, when the weight ratio nickel/cobalt exceeds 0.15 or 0.2, the advantageous chemical and electrochemical properties of cobalt oxide CoO tend to disappear. Therefore, the nickel content should not exceed this limit.
In one embodiment, the anode comprises an oxygen barrier layer between the CoO-containing layer and the electrically conductive substrate. The oxygen barrier layer can contain at least one metal selected from nickel, copper, tungsten, molybdenum, tantalum, niobium and chromium, or an oxide thereof, for example alloyed with cobalt, such as a cobalt alloy containing tungsten, molybdenum, tantalum and/or niobium, in particular an alloy containing: at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wto, such as 10 to 20 wt%; and one or more further elements and compounds in a total amount of up to 5 wt%
such as 0.01 to 4 weighto, the balance being cobalt.
These further elements may contain at least one of aluminium, silicon and manganese.
Typically, the oxygen barrier layer and the CoO-containing layer are formed by oxidising the surface of an applied layer of the abovementioned cobalt alloy that contains nickel, tungsten, molybdenum, tantalum and/or niobium. The resulting CoO-containing layer is predominantly made of CoO and is integral with the unoxidised part of the metallic cobalt alloy that forms the oxygen barrier layer.
When the CoO layer is integral with the cobalt alloy, the nickel, when present, should be contained in the alloy in an amount of up to 20 weight%, in particular 5 to 15 weight%. Such an amount of nickel in the alloy leads to the formation of a small amount of nickel oxide NiO in the integral oxide layer, in about the same proportions to cobalt as in the metallic part, i.e. 5 to 15 or 20 weight%. It has been observed that the presence of a small amount of nickel oxide stabilises the cobalt oxide CoO and durably inhibits the formation of Co2O3 or Co3O4. However, when the weight ratio nickel/cobalt exceeds 0.15 or 0.2, the advantageous chemical and electrochemical properties of cobalt oxide CoO tend to disappear. Therefore, the nickel content should not exceed this limit.
- 13 -Alternatively, an oxygen barrier layer, for example made of the above cobalt alloy that contains nickel, tungsten, molybdenum, tantalum and/or niobium, can be covered with an applied layer of CoO or a precursor thereof, as discussed above. In this case the oxygen barrier layer can be an applied layer or it can be integral with the electrically conductive substrate.
In another embodiment, the Co-containing metallic layer consists essentially of cobalt, typically containing cobalt in an amount of at least 95 wt%, in particular more than 97 wt% or 99 wt%.
Optionally the Co-containing metallic layer contains at least one additive selected from silicon, nickel, manganese, niobium, tantalum and aluminium in a total amount of 0.1 to 2 wt%.
Such a Co-containing layer can be applied to an oxygen barrier layer which is integral with the electrically conductive substrate of the flow-through anode structure or applied thereto.
The electrically conductive substrate can comprise.
at least one metal selected from chromium, cobalt, hafnium, iron, molybdenum, nickel, copper, platinum, silicon, titanium, tungsten, molybdenum, tantalum, niobium, vanadium, yttrium and zirconium, or a compound thereof, in particular an oxide, or a combination thereof. For instance, the electrically conductive substrate may have an outer part made of cobalt or an alloy containing predominantly cobalt to which the coating is applied. For instance, this cobalt alloy contains nickel, tungsten, molybdenum, tantalum and/or niobium, in particular it contains: nickel tungsten, molybdenum, tantalum and/or niobium in a total amount of 5 to 30 wt%, e.g. 10 to 20 wt%; and one or more further elements and/or compounds in a total amount of up to 5 wt%, the balance being cobalt. These further elements may contain at least one of aluminium, silicon and manganese.
The electrically conductive substrate, or an outer part thereof, may contain or consist essentially of at least one oxidation-resistant metal, in particular one or more metals selected from nickel, tungsten, molybdenum,
In another embodiment, the Co-containing metallic layer consists essentially of cobalt, typically containing cobalt in an amount of at least 95 wt%, in particular more than 97 wt% or 99 wt%.
Optionally the Co-containing metallic layer contains at least one additive selected from silicon, nickel, manganese, niobium, tantalum and aluminium in a total amount of 0.1 to 2 wt%.
Such a Co-containing layer can be applied to an oxygen barrier layer which is integral with the electrically conductive substrate of the flow-through anode structure or applied thereto.
The electrically conductive substrate can comprise.
at least one metal selected from chromium, cobalt, hafnium, iron, molybdenum, nickel, copper, platinum, silicon, titanium, tungsten, molybdenum, tantalum, niobium, vanadium, yttrium and zirconium, or a compound thereof, in particular an oxide, or a combination thereof. For instance, the electrically conductive substrate may have an outer part made of cobalt or an alloy containing predominantly cobalt to which the coating is applied. For instance, this cobalt alloy contains nickel, tungsten, molybdenum, tantalum and/or niobium, in particular it contains: nickel tungsten, molybdenum, tantalum and/or niobium in a total amount of 5 to 30 wt%, e.g. 10 to 20 wt%; and one or more further elements and/or compounds in a total amount of up to 5 wt%, the balance being cobalt. These further elements may contain at least one of aluminium, silicon and manganese.
The electrically conductive substrate, or an outer part thereof, may contain or consist essentially of at least one oxidation-resistant metal, in particular one or more metals selected from nickel, tungsten, molybdenum,
- 14 -cobalt, chromium and niobium, and for example contains less than 1, 5 or 10 wt% in total of other metals and metal compounds, in particular oxides. Alternatively, the electrically conductive substrate can be made of an alloy of nickel, iron and copper, in particular an alloy containing: 65 to 85 weight% nickel; 5 to 25 weight%
iron; 1 to 20 weight% copper; and 0 to 10 weight% further constituents. For example, the alloy contains about: 75 weight% nickel; 15 weight% iron; and 10 weight% copper.
Advantageously, the anode's Co0-containing layer, in particular when the CoO layer is integral with the applied Co-containing metallic layer or the anode body, has an open porosity of below 12%, such as below 7%.
The anode's Co0-containing layer can have a porosity with an average pore size below 7 micron, in particular below 4 micron. It is preferred to provide a substantially crack-free Co0-containing layer so as to protect efficiently the anode's metallic outer part which is covered by this CoO-containing layer.
Usually, the Co0-containing layer contains cobalt oxide CoO in an amount of at least=80 wt%, in particular more than 90 wt% or 95 wt% or 98 wt%.
Advantageously, the Co0-containing layer is substantially free of cobalt oxide Co203 and substantially free of Co3O4, and contains preferably below 3 or 1.5% of these forms of cobalt oxide.
The Co0-containing layer may be electrochemically active for the oxidation of oxygen ions during use, in which case this layer is uncovered or is covered with an electrolyte-pervious layer.
Alternatively, the CoO-containing layer can be covered with an applied protective layer, in particular an applied oxide layer such as a layer containing cobalt and/or iron oxide, e.g. cobalt ferrite. The applied protective layer'may contain a pre-formed and/or in-situ deposited cerium compound, in particular cerium oxyfluoride, as for example disclosed in the abovementioned US patents 4,956,069, 4,960,494 and
iron; 1 to 20 weight% copper; and 0 to 10 weight% further constituents. For example, the alloy contains about: 75 weight% nickel; 15 weight% iron; and 10 weight% copper.
Advantageously, the anode's Co0-containing layer, in particular when the CoO layer is integral with the applied Co-containing metallic layer or the anode body, has an open porosity of below 12%, such as below 7%.
The anode's Co0-containing layer can have a porosity with an average pore size below 7 micron, in particular below 4 micron. It is preferred to provide a substantially crack-free Co0-containing layer so as to protect efficiently the anode's metallic outer part which is covered by this CoO-containing layer.
Usually, the Co0-containing layer contains cobalt oxide CoO in an amount of at least=80 wt%, in particular more than 90 wt% or 95 wt% or 98 wt%.
Advantageously, the Co0-containing layer is substantially free of cobalt oxide Co203 and substantially free of Co3O4, and contains preferably below 3 or 1.5% of these forms of cobalt oxide.
The Co0-containing layer may be electrochemically active for the oxidation of oxygen ions during use, in which case this layer is uncovered or is covered with an electrolyte-pervious layer.
Alternatively, the CoO-containing layer can be covered with an applied protective layer, in particular an applied oxide layer such as a layer containing cobalt and/or iron oxide, e.g. cobalt ferrite. The applied protective layer'may contain a pre-formed and/or in-situ deposited cerium compound, in particular cerium oxyfluoride, as for example disclosed in the abovementioned US patents 4,956,069, 4,960,494 and
- 15 -5,069,771. Such an applied protective layer is usually electrochemically active for the oxidation of oxygen ions and is uncovered, or covered in turn with an electrolyte pervious-layer.
The anode's electrochemically active surface can contain at least one dopant, in particular at least one dopant selected from iridium, palladium, platinum, rhodium, ruthenium, silicon, tungsten, molybdenum, tantalum, niobium, tin or zinc metals, Mischmetal and metals of the Lanthanide series, as metals and compounds, in particular oxides, and mixtures thereof. The dopant(s) can be present at the anode's surface in a total amount of 0.1 to 5 wt%, in particular 1 to 4 wt%.
Such a dopant can be an electrocatalyst for fostering the oxidation of oxygen ions on the anode's electrochemically active surface and/or can contribute to inhibit diffusion of oxygen ions into the anode.
The dopant may be added to the precursor material that is applied to form the active surface or it can be applied to the active surface as a thin film, for example by plasma spraying or slurry application, and incorporated into the surface by heat treatment.
The cell can have a cathode that has an aluminium-wettable surface, in particular a horizontal or inclined drained surface. This surface can be formed by an aluminium-wettable material that comprises a refractory boride and/or an aluminium-wetting oxide. Examples of such materials are disclosed in WO01/42168, WO01/42531, W002/070783, W002/096830 and W002/096831 (all in the name of MOLTECH).
The anode can be suspended in the electrolyte by a stem, in particular a stem having an outer part comprising a layer that contains predominantly cobalt oxide CoO.
Another aspect of the invention relates to a method of electrowinning aluminium in a cell as described above The method comprises electrolysing the dissolved alumina to produce oxygen on the anode and aluminium
The anode's electrochemically active surface can contain at least one dopant, in particular at least one dopant selected from iridium, palladium, platinum, rhodium, ruthenium, silicon, tungsten, molybdenum, tantalum, niobium, tin or zinc metals, Mischmetal and metals of the Lanthanide series, as metals and compounds, in particular oxides, and mixtures thereof. The dopant(s) can be present at the anode's surface in a total amount of 0.1 to 5 wt%, in particular 1 to 4 wt%.
Such a dopant can be an electrocatalyst for fostering the oxidation of oxygen ions on the anode's electrochemically active surface and/or can contribute to inhibit diffusion of oxygen ions into the anode.
The dopant may be added to the precursor material that is applied to form the active surface or it can be applied to the active surface as a thin film, for example by plasma spraying or slurry application, and incorporated into the surface by heat treatment.
The cell can have a cathode that has an aluminium-wettable surface, in particular a horizontal or inclined drained surface. This surface can be formed by an aluminium-wettable material that comprises a refractory boride and/or an aluminium-wetting oxide. Examples of such materials are disclosed in WO01/42168, WO01/42531, W002/070783, W002/096830 and W002/096831 (all in the name of MOLTECH).
The anode can be suspended in the electrolyte by a stem, in particular a stem having an outer part comprising a layer that contains predominantly cobalt oxide CoO.
Another aspect of the invention relates to a method of electrowinning aluminium in a cell as described above The method comprises electrolysing the dissolved alumina to produce oxygen on the anode and aluminium
16 PCT/IB2005/051718 cathodically, and supplying alumina to the electrolyte to maintain therein a concentration of dissolved alumina of 6.5 to 11 weight%, in particular 7 to 10 weight%.
Oxygen ions may be oxidised on the anode's CoO-containing layer that contains predominantly cobalt oxide CoO and/or, when present, on an active layer applied to the anode's CoO layer, the Co0 layer inhibiting oxidation and/or corrosion of the anode's metallic outer part.
The invention also relates to a non-carbon metal-based anode for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte. This anode comprises an electrically conductive metallic structure that comprises an outer part with an=electrochemically active anode surface on which oxygen is anodically evolved and which is suspended in the electrolyte substantially parallel to a facing cathode during use. This metallic structure has one or more flow-through openings extending from the active anode surface through the metallic structure. These flow-through opening(s) are arranged for guiding during use a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises the abovementioned layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode. This anode can include any of the above described anode features or a combination thereof.
Brief Description of the Drawings The invention will now be described with reference to the schematic drawings, wherein:
- Figures la and lb show respectively a side elevation and a plan view of an anode according to the invention;
- Figures 2a and 2b show respectively a side elevation and a plan view of another anode according to the invention;
- Figures 3, 4, 5 and 6 show side elevations of variations of the anode shown in Figures la and lb;
Oxygen ions may be oxidised on the anode's CoO-containing layer that contains predominantly cobalt oxide CoO and/or, when present, on an active layer applied to the anode's CoO layer, the Co0 layer inhibiting oxidation and/or corrosion of the anode's metallic outer part.
The invention also relates to a non-carbon metal-based anode for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte. This anode comprises an electrically conductive metallic structure that comprises an outer part with an=electrochemically active anode surface on which oxygen is anodically evolved and which is suspended in the electrolyte substantially parallel to a facing cathode during use. This metallic structure has one or more flow-through openings extending from the active anode surface through the metallic structure. These flow-through opening(s) are arranged for guiding during use a circulation of electrolyte driven by the fast escape of anodically evolved oxygen. The outer part of the anode comprises the abovementioned layer that contains predominantly cobalt oxide CoO to enhance the stability of the anode. This anode can include any of the above described anode features or a combination thereof.
Brief Description of the Drawings The invention will now be described with reference to the schematic drawings, wherein:
- Figures la and lb show respectively a side elevation and a plan view of an anode according to the invention;
- Figures 2a and 2b show respectively a side elevation and a plan view of another anode according to the invention;
- Figures 3, 4, 5 and 6 show side elevations of variations of the anode shown in Figures la and lb;
- 17 -- Figures 7 and 8 show cross-sections of multi-part anode members according to the invention;
- Figure 9 shows an aluminium electrowinning cell operating with anodes according to the invention fitted with electrolyte guide members;
- Figures 10, 11 and 12 are enlarged views of parts of variations of the electrolyte guide members shown in Figure 9, Figure 10 illustrating cell operation;
- Figure 13 is a cross section of another anode according to the invention with electrolyte guide members only one of which is shown;
- Figure 14 shows a plan view of half of an assembly of several electrolyte guide members like the one shown in Figure 13;
- Figure 15 is a plan view of the anode shown Figure 13 with half of an assembly of electrolyte guide members as shown in Figure 14; and - Figure 16 is a plan view of a variation of the anode of Figure 15.
Detailed Description Figures la and lb schematically show an anode 10 of a cell for the electrowinning of aluminium according to the invention.
The anode 10 comprises a vertical current feeder 11 for connecting the anode to a positive bus bar, a cross member 12 and a pair of transverse connecting members 13 for connecting a series of anode members 15.
The anode members 15 have an electrochemically active lower surface 16 where oxygen is anodically evolved during cell operation. The anode members 15 are in the form of parallel rods in a coplanar arrangement, laterally spaced apart from one another by inter-member gaps 17. The inter-member gaps 17 constitute flow-through openings for the circulation of electrolyte and the
- Figure 9 shows an aluminium electrowinning cell operating with anodes according to the invention fitted with electrolyte guide members;
- Figures 10, 11 and 12 are enlarged views of parts of variations of the electrolyte guide members shown in Figure 9, Figure 10 illustrating cell operation;
- Figure 13 is a cross section of another anode according to the invention with electrolyte guide members only one of which is shown;
- Figure 14 shows a plan view of half of an assembly of several electrolyte guide members like the one shown in Figure 13;
- Figure 15 is a plan view of the anode shown Figure 13 with half of an assembly of electrolyte guide members as shown in Figure 14; and - Figure 16 is a plan view of a variation of the anode of Figure 15.
Detailed Description Figures la and lb schematically show an anode 10 of a cell for the electrowinning of aluminium according to the invention.
The anode 10 comprises a vertical current feeder 11 for connecting the anode to a positive bus bar, a cross member 12 and a pair of transverse connecting members 13 for connecting a series of anode members 15.
The anode members 15 have an electrochemically active lower surface 16 where oxygen is anodically evolved during cell operation. The anode members 15 are in the form of parallel rods in a coplanar arrangement, laterally spaced apart from one another by inter-member gaps 17. The inter-member gaps 17 constitute flow-through openings for the circulation of electrolyte and the
- 18 -escape of anodically-evolved gas released at the electrochemically active surfaces 16.
The anode members 15 are transversally connected by the pair of transverse connecting members 13 which are in turn connected together by the cross member 12 on which the vertical current feeder 11 is mounted. The current feeder 11, the cross member 12, the transverse connecting members 13 and the anode members 15 are mechanically secured together by welding, rivets or other means.
In accordance with the invention, the electrochemically active surface 16 of the anode members is formed by an outer part that comprises a layer containing predominantly CoO. This CoO layer can form the electrochemically active surface 16 and be directly 15 exposed to the electrolyte during use or the CoO layer can be covered with a further layer, for instance a layer containing predominantly a cerium compound such as cerium oxyfluoride.
The cross-member 12 and the transverse connecting members 13 are so designed and positioned over the anode members 15 to provide a substantially even current distribution through the anode members 15 to their electrochemically active surfaces 16. The current feeder 11, the cross-member 12 and the transverse connecting members 13 do not need to be electrochemically active and their surface may passivate when exposed to electrolyte.
However they should be electrically well conductive to avoid unnecessary voltage drops and should not substantially dissolve in electrolyte. The electrochemically-inactive current-carrying elements (11,12,13) can have an outer part with a protective layer containing predominantly CoO.
Figures 2a and 2b schematically show a variation of the anode 10 shown in Figures la and lb.
Instead of having transverse connecting members 13, a cross-member 12 and a current feeder 11 for mechanically and electrically connecting the anode members 15 to a positive bus bar as illustrated in Figures la and lb, the anode 10 shown in Figures 2a and
The anode members 15 are transversally connected by the pair of transverse connecting members 13 which are in turn connected together by the cross member 12 on which the vertical current feeder 11 is mounted. The current feeder 11, the cross member 12, the transverse connecting members 13 and the anode members 15 are mechanically secured together by welding, rivets or other means.
In accordance with the invention, the electrochemically active surface 16 of the anode members is formed by an outer part that comprises a layer containing predominantly CoO. This CoO layer can form the electrochemically active surface 16 and be directly 15 exposed to the electrolyte during use or the CoO layer can be covered with a further layer, for instance a layer containing predominantly a cerium compound such as cerium oxyfluoride.
The cross-member 12 and the transverse connecting members 13 are so designed and positioned over the anode members 15 to provide a substantially even current distribution through the anode members 15 to their electrochemically active surfaces 16. The current feeder 11, the cross-member 12 and the transverse connecting members 13 do not need to be electrochemically active and their surface may passivate when exposed to electrolyte.
However they should be electrically well conductive to avoid unnecessary voltage drops and should not substantially dissolve in electrolyte. The electrochemically-inactive current-carrying elements (11,12,13) can have an outer part with a protective layer containing predominantly CoO.
Figures 2a and 2b schematically show a variation of the anode 10 shown in Figures la and lb.
Instead of having transverse connecting members 13, a cross-member 12 and a current feeder 11 for mechanically and electrically connecting the anode members 15 to a positive bus bar as illustrated in Figures la and lb, the anode 10 shown in Figures 2a and
- 19 -2b comprises a pair of cast or profiled support members 14 fulfilling the same function. Each cast support member 14 comprises a lower horizontally extending foot 14a for electrically and mechanically connecting the anode members 15, a stem 14b for connecting the anode 10 to a positive bus bar and a pair of lateral reinforcement flanges 14c between the horizontally extending foot 14a and stem 14b.
The anode members 15 may be secured by force-fitting or welding in the horizontal foot 14a. As an alternative, the shape of the anode members 15 and corresponding receiving slots in the foot 14a may be such as to allow only longitudinal movements of the anode members. For instance the anode members 15 and the foot 14a may be connected by dovetail joints.
Figures 3 to 6 show a series of anodes 10 according to the invention which are similar to the anode 10 shown in Figures la and lb. However the cross-sections of the anode members 15 of the anodes 10 shown in Figures 3 to 6 differ to the circular cross-section of the anode members 10 shown in Figures la and lb.
The anode members 15 of the anode shown in Figure 3 have in cross-section a generally semi-circular upper part and a flat bottom which constitutes the electrochemically active surface 16 of each anode member 15.
Figure 4 illustrates anode members 15 in the form of rods which have a generally bell-shaped or pear-shaped cross-section. The electrochemically active surface 16 of the anode members 10 is located along the bottom of the bell-shape or pear-shape.
The anode members 15 shown in Figure 5 are rods having a generally rectangular cross-section. The electrochemically active surface 16 is located along the bottom narrow side of the rod.
Figures 6 and 7 show an anode 10 having assembled multi-part anode members 15 comprising a first member 15b supporting an electrochemically active second member 15a.
The anode members 15 may be secured by force-fitting or welding in the horizontal foot 14a. As an alternative, the shape of the anode members 15 and corresponding receiving slots in the foot 14a may be such as to allow only longitudinal movements of the anode members. For instance the anode members 15 and the foot 14a may be connected by dovetail joints.
Figures 3 to 6 show a series of anodes 10 according to the invention which are similar to the anode 10 shown in Figures la and lb. However the cross-sections of the anode members 15 of the anodes 10 shown in Figures 3 to 6 differ to the circular cross-section of the anode members 10 shown in Figures la and lb.
The anode members 15 of the anode shown in Figure 3 have in cross-section a generally semi-circular upper part and a flat bottom which constitutes the electrochemically active surface 16 of each anode member 15.
Figure 4 illustrates anode members 15 in the form of rods which have a generally bell-shaped or pear-shaped cross-section. The electrochemically active surface 16 of the anode members 10 is located along the bottom of the bell-shape or pear-shape.
The anode members 15 shown in Figure 5 are rods having a generally rectangular cross-section. The electrochemically active surface 16 is located along the bottom narrow side of the rod.
Figures 6 and 7 show an anode 10 having assembled multi-part anode members 15 comprising a first member 15b supporting an electrochemically active second member 15a.
- 20 -The electrochemically active member 15a has an electrochemically active surface 16 and is connected along it whole length to the electrically well-conductive support member 15b by an intermediate connecting member 15c such as a flange.
Figure 7 shows an enlarged view of the assembled anode member 15 of Figure 6, comprising a generally cylindrical electrochemically active member 15a with an electrochemically active surface 16, a generally cylindrical electrically conductive support member 15b and an intermediate connecting member or flange 15c electrically and mechanically connecting the support member 15b to the electrochemically active member 15a.
Alternatively, the connecting member 15c may be an extension of either the electrochemically active member 15a or the support member 15b as shown in Figure 8.
The intermediate connecting member 15c shown in Figure 7 may be connected to the electrochemically active member 15a and to the support member 15b by force-fitting or welding. However, these parts may be mechanically connected by providing a suitable geometry of the connecting members 15c and the corresponding receiving slots of the electrochemically active member 15a and the support member 15b, for instance with dovetail joints.
In accordance with the invention, the electrochemically active member 15a shown in Figures 7 and 8 has an outer part that comprises a layer containing predominantly CoO. As mentioned above, this CoO layer can form the electrochemically active surface 16 and be directly exposed to the electrolyte during use or the CoO
layer can be covered with a further layer, for instance a layer containing predominantly a cerium compound such as cerium oxyfluoride.
The support member 15b shown in Figures 7 and 8 and the connecting member 15c shown in Figure 7 are preferably highly conductive and may comprise a metallic core, for instance nickel covered with an oxidised cobalt layer (having a CoO-based surface).
Figure 7 shows an enlarged view of the assembled anode member 15 of Figure 6, comprising a generally cylindrical electrochemically active member 15a with an electrochemically active surface 16, a generally cylindrical electrically conductive support member 15b and an intermediate connecting member or flange 15c electrically and mechanically connecting the support member 15b to the electrochemically active member 15a.
Alternatively, the connecting member 15c may be an extension of either the electrochemically active member 15a or the support member 15b as shown in Figure 8.
The intermediate connecting member 15c shown in Figure 7 may be connected to the electrochemically active member 15a and to the support member 15b by force-fitting or welding. However, these parts may be mechanically connected by providing a suitable geometry of the connecting members 15c and the corresponding receiving slots of the electrochemically active member 15a and the support member 15b, for instance with dovetail joints.
In accordance with the invention, the electrochemically active member 15a shown in Figures 7 and 8 has an outer part that comprises a layer containing predominantly CoO. As mentioned above, this CoO layer can form the electrochemically active surface 16 and be directly exposed to the electrolyte during use or the CoO
layer can be covered with a further layer, for instance a layer containing predominantly a cerium compound such as cerium oxyfluoride.
The support member 15b shown in Figures 7 and 8 and the connecting member 15c shown in Figure 7 are preferably highly conductive and may comprise a metallic core, for instance nickel covered with an oxidised cobalt layer (having a CoO-based surface).
- 21 -Figure 9 shows an aluminium electrowinning cell according to the invention having a series of generally horizontal anodes 10 which are similar to those shown in Figures la and lb, immersed in an electrolyte 30. The anodes 10 face a horizontal cathode cell bottom 20 connected to a negative busbar by current conductor bars 21. The cathode cell bottom 20 is made of conductive material such as graphite or other carbonaceous material coated with an aluminium-wettable refractory cathodic coating 22 on which aluminium 35 is produced and from which it drains or on which it forms a shallow pool, a deep pool or a stabilised pool. The molten aluminium 35 produced is spaced apart from the facing anodes 10 by an inter-electrode gap.
Pairs of anodes 10 are connected to a positive bus bar through a primary vertical current feeder 11' and a horizontal current distributor 11" connected at both of its ends to a foraminate anode 10 through a secondary vertical current distributor il"'.
The secondary vertical current distributor 11"' is mounted on the anode structure 12,13,15, on a cross member 12 which is in turn connected to a pair of transverse connecting members 13 for connecting a series of anode members 15. The current feeders 11',11",11"', the cross member 12, the transverse connecting members 13 and the anode members 15 are mechanically secured together by welding, rivets or other means.
The anode members 15 have an electrochemically active lower surface 16 on which during cell operation oxygen is anodically evolved. The anode members 15 are in the form of parallel rods in a foraminate coplanar arrangement, laterally spaced apart from one another by inter-member gaps 17. The inter-member gaps 17 constitute flow-through openings for the circulation of electrolyte and the escape of anodically-evolved gas from the electrochemically active surfaces 16.
The cross-member 12 and the transverse connecting members 13 provide a substantially even current distribution through the anode members 15 to their electrochemically active surfaces 16. The current feeder
Pairs of anodes 10 are connected to a positive bus bar through a primary vertical current feeder 11' and a horizontal current distributor 11" connected at both of its ends to a foraminate anode 10 through a secondary vertical current distributor il"'.
The secondary vertical current distributor 11"' is mounted on the anode structure 12,13,15, on a cross member 12 which is in turn connected to a pair of transverse connecting members 13 for connecting a series of anode members 15. The current feeders 11',11",11"', the cross member 12, the transverse connecting members 13 and the anode members 15 are mechanically secured together by welding, rivets or other means.
The anode members 15 have an electrochemically active lower surface 16 on which during cell operation oxygen is anodically evolved. The anode members 15 are in the form of parallel rods in a foraminate coplanar arrangement, laterally spaced apart from one another by inter-member gaps 17. The inter-member gaps 17 constitute flow-through openings for the circulation of electrolyte and the escape of anodically-evolved gas from the electrochemically active surfaces 16.
The cross-member 12 and the transverse connecting members 13 provide a substantially even current distribution through the anode members 15 to their electrochemically active surfaces 16. The current feeder
- 22 -11, the cross-member 12 and the transverse connecting members 13 do not need to be electrochemically active and their surface may passivate when exposed to electrolyte.
However they should be electrically well conductive to avoid unnecessary voltage drops and should not substantially dissolve in the molten electrolyte.
In accordance with the invention, the active surface 16 of the anode members 15 can be CoO-based.
The CoO-based surface may extend over all immersed parts 11"',12,13,15 of the anode 10, in particular over the immersed part of the secondary vertical current distributor 11"' which is preferably covered with a CoO-based layer at least up to 10 cm above the surface of the electrolyte 30.
The anodes 10 are further fitted with means for enhancing dissolution of fed alumina in the form of electrolyte guide members 5 formed of parallel spaced-apart inclined baffles 5 located above and adjacent to the foraminate anode structure 12,13,15. The baffles 5 provide upper downwardly converging surfaces 6 and lower upwardly converging surfaces 7 that deflect gaseous oxygen which is anodically produced below, the electrochemically active surface 16 of the anode members 15 and which escapes between the inter-member gaps 17 through the foraminate anode structure 12,13,15. The oxygen released above the baffles 5 promotes dissolution of alumina fed into the electrolyte 30 above the downwardly converging surfaces 6. Further details of such baffles are disclosed in the abovementioned W000/40781 and W000/40782.
The aluminium-wettable cathodic coating 22 of the cell shown in Figure 9 can advantageously be a slurry-applied refractory hard metal coating as disclosed in US
Patent WO01/42534 (de Nora/Duruz), WO01/42531 (Nguyen/
Duruz/de Nora) and W002/096831 (Nguyen/de Nora).
During cell operation, alumina is fed to the electrolyte 30 all over the baffles 5 and the metallic anode structure 12,13,15. The fed alumina is dissolved and distributed from the bottom end of the converging -e
However they should be electrically well conductive to avoid unnecessary voltage drops and should not substantially dissolve in the molten electrolyte.
In accordance with the invention, the active surface 16 of the anode members 15 can be CoO-based.
The CoO-based surface may extend over all immersed parts 11"',12,13,15 of the anode 10, in particular over the immersed part of the secondary vertical current distributor 11"' which is preferably covered with a CoO-based layer at least up to 10 cm above the surface of the electrolyte 30.
The anodes 10 are further fitted with means for enhancing dissolution of fed alumina in the form of electrolyte guide members 5 formed of parallel spaced-apart inclined baffles 5 located above and adjacent to the foraminate anode structure 12,13,15. The baffles 5 provide upper downwardly converging surfaces 6 and lower upwardly converging surfaces 7 that deflect gaseous oxygen which is anodically produced below, the electrochemically active surface 16 of the anode members 15 and which escapes between the inter-member gaps 17 through the foraminate anode structure 12,13,15. The oxygen released above the baffles 5 promotes dissolution of alumina fed into the electrolyte 30 above the downwardly converging surfaces 6. Further details of such baffles are disclosed in the abovementioned W000/40781 and W000/40782.
The aluminium-wettable cathodic coating 22 of the cell shown in Figure 9 can advantageously be a slurry-applied refractory hard metal coating as disclosed in US
Patent WO01/42534 (de Nora/Duruz), WO01/42531 (Nguyen/
Duruz/de Nora) and W002/096831 (Nguyen/de Nora).
During cell operation, alumina is fed to the electrolyte 30 all over the baffles 5 and the metallic anode structure 12,13,15. The fed alumina is dissolved and distributed from the bottom end of the converging -e
- 23 -surfaces 6 into the inter-electrode gap through the inter-member gaps 17 and around edges of the metallic anode structure 12,13,15, i.e. between neighbouring pairs of anodes 10 or between peripheral anodes 10 and sidewalls 25. By passing an electric current between anodes 10 and facing cathode cell bottom 20 oxygen is evolved on the electrochemically active anode surfaces 16 and aluminium is produced which is incorporated into the cathodic molten aluminium 35. The oxygen evolved from the active surfaces 16 escapes through the inter-member gaps 17 and is deflected by the upwardly converging surfaces 7 of baffles 5. The oxygen escapes from the uppermost ends of the upwardly converging surfaces 7 enhancing dissolution of the alumina fed over the downwardly converging surfaces 6.
The aluminium electrowinning cells partly shown in Figures 10, 11 and 12 are similar to the aluminium electrowinning cell shown in Figure 9.
In Figure 10 the guide members are inclined baffles 5 as shown in Figure 9. In this example the uppermost end of each baffle 5 is located just above mid-height between the surface of the electrolyte 30 and the transverse connecting members 13.
Also shown in Fig. 10, an electrolyte circulation 31 is generated by the escape of gas released from the active surfaces 16 of the anode members 15 between the inter-member gaps 17 and which is deflected by the upward converging surfaces 7 of the baffles 5 confining the gas and the electrolyte flow between their uppermost edges.
From the uppermost edges of the baffles 5, the anodically evolved gas escapes towards the surface of the electrolyte 30, whereas the electrolyte circulation 31 flows down through the downward converging surfaces 6, through the inter-member gaps and around edges of the metallic anode structure 12,13,15 to compensate the depression created by the anodically released gas below the active surfaces 17 of the anode members 15. The electrolyte circulation 31 draws down into the inter-electrode gap dissolving alumina particles 32 which are fed above the downward converging surfaces 6.
The aluminium electrowinning cells partly shown in Figures 10, 11 and 12 are similar to the aluminium electrowinning cell shown in Figure 9.
In Figure 10 the guide members are inclined baffles 5 as shown in Figure 9. In this example the uppermost end of each baffle 5 is located just above mid-height between the surface of the electrolyte 30 and the transverse connecting members 13.
Also shown in Fig. 10, an electrolyte circulation 31 is generated by the escape of gas released from the active surfaces 16 of the anode members 15 between the inter-member gaps 17 and which is deflected by the upward converging surfaces 7 of the baffles 5 confining the gas and the electrolyte flow between their uppermost edges.
From the uppermost edges of the baffles 5, the anodically evolved gas escapes towards the surface of the electrolyte 30, whereas the electrolyte circulation 31 flows down through the downward converging surfaces 6, through the inter-member gaps and around edges of the metallic anode structure 12,13,15 to compensate the depression created by the anodically released gas below the active surfaces 17 of the anode members 15. The electrolyte circulation 31 draws down into the inter-electrode gap dissolving alumina particles 32 which are fed above the downward converging surfaces 6.
- 24 -Figure 11 shows part of an aluminium electrowinning cell with baffles 5 operating as electrolyte guide members like those shown in cell of Figure 9 but whose surfaces are only partly converging. The lower sections,4 of the baffles 5 are vertical and parallel to one another, whereas their upper sections have upward and downward converging surfaces 6,7. The uppermost end of the baffles 5 are located below but close to the surface of the electrolyte 30 to increase the turbulence at the electrolyte surface caused by the release of anodically evolved gas.
Figure 12 shows a variation of the baffles shown in Figure 11, wherein parallel vertical sections 4 are located above the converging surfaces 6,7.
By guiding and confining anodically-evolved oxygen towards the surface of the electrolyte 30 with baffles or other confinement means as shown in Figures 11 and 12, oxygen is released so close to the surface as to create turbulences above the downwardly converging surfaces 6, promoting dissolution of alumina fed thereabove.
It is understood that the electrolyte confinement members 5 shown in Figures 9, 10, 11 and 12 can either be elongated baffles, or instead consist of a series of vertical chimneys of funnels of circular or polygonal cross-section, for instance as described below.
Figures 13 and 15 illustrate an anode 10' having a circular bottom, the anode 10' being shown in cross-section in Figure 5 and from above in Figure 15. On the right hand side of Figures 13 and 15 the anode 10' is shown with electrolyte guide members 5'. The electrolyte guide members 5' represented in Figure 15 are shown separately in Figure 14.
The anode 10' shown in Figures 13 and 15 has several concentric circular anode members 15. The anode members 15 are laterally spaced apart from one another by inter-member gaps 17 and connected together by radial connecting members in the form of flanges 13 which join an outer ring 13'. The outer ring 13' extends vertically from the outermost anode members 15, as shown in Figure
Figure 12 shows a variation of the baffles shown in Figure 11, wherein parallel vertical sections 4 are located above the converging surfaces 6,7.
By guiding and confining anodically-evolved oxygen towards the surface of the electrolyte 30 with baffles or other confinement means as shown in Figures 11 and 12, oxygen is released so close to the surface as to create turbulences above the downwardly converging surfaces 6, promoting dissolution of alumina fed thereabove.
It is understood that the electrolyte confinement members 5 shown in Figures 9, 10, 11 and 12 can either be elongated baffles, or instead consist of a series of vertical chimneys of funnels of circular or polygonal cross-section, for instance as described below.
Figures 13 and 15 illustrate an anode 10' having a circular bottom, the anode 10' being shown in cross-section in Figure 5 and from above in Figure 15. On the right hand side of Figures 13 and 15 the anode 10' is shown with electrolyte guide members 5'. The electrolyte guide members 5' represented in Figure 15 are shown separately in Figure 14.
The anode 10' shown in Figures 13 and 15 has several concentric circular anode members 15. The anode members 15 are laterally spaced apart from one another by inter-member gaps 17 and connected together by radial connecting members in the form of flanges 13 which join an outer ring 13'. The outer ring 13' extends vertically from the outermost anode members 15, as shown in Figure
- 25 -13, to form with the radial flanges 13 a wheel-like structure 13,13', shown in Figure 15, which secures the anode members 15 to a central anode current feeder 11.
As shown in Figure 13, the innermost circular anode member 15 partly merges with the current feeder 11, with ducts 18 extending between the innermost circular anode member 15 and the current feeder 11 to permit the escape of oxygen produced underneath the central current feeder 11.
Each electrolyte guide member 5' is in the general shape of a funnel having a wide bottom opening 9 for receiving anodically produced oxygen and a narrow top opening 8 where the oxygen is released to promote dissolution of alumina fed above the electrolyte guide member 5'. The inner surface 7 of the electrolyte guide member 5' is arranged to canalise and promote an upward electrolyte flow driven by anodically produced oxygen.
The outer surface 6 of the electrolyte guide member 5' is arranged to promote dissolution of alumina fed thereabove and guide alumina-rich electrolyte down to the inter-electrode gap, the electrolyte flowing mainly around the foraminate structure.
As shown in Figures 14 and 15, the electrolyte guide members 5' are in a circular arrangement, only half of the arrangement being shown. The electrolyte guide members 5' are laterally secured to one another by attachments 3 and so arranged to be held above the anode members 15, the attachments 3 being for example placed on the flanges 13 as shown in Figure 15 or secured as required. Each electrolyte guide member 5' is positioned in a circular sector defined by two neighbouring radial flanges 13 and an arc of the outer ring 13' as shown in Figure 15.
The arrangement of the electrolyte guide members 5' and the anode 10' can be moulded as units. This offers the advantage of avoiding mechanical joints and the risk of altering the properties of the materials of the electrolyte guide members 5' or the anode 10' by welding.
As shown in Figure 13, the innermost circular anode member 15 partly merges with the current feeder 11, with ducts 18 extending between the innermost circular anode member 15 and the current feeder 11 to permit the escape of oxygen produced underneath the central current feeder 11.
Each electrolyte guide member 5' is in the general shape of a funnel having a wide bottom opening 9 for receiving anodically produced oxygen and a narrow top opening 8 where the oxygen is released to promote dissolution of alumina fed above the electrolyte guide member 5'. The inner surface 7 of the electrolyte guide member 5' is arranged to canalise and promote an upward electrolyte flow driven by anodically produced oxygen.
The outer surface 6 of the electrolyte guide member 5' is arranged to promote dissolution of alumina fed thereabove and guide alumina-rich electrolyte down to the inter-electrode gap, the electrolyte flowing mainly around the foraminate structure.
As shown in Figures 14 and 15, the electrolyte guide members 5' are in a circular arrangement, only half of the arrangement being shown. The electrolyte guide members 5' are laterally secured to one another by attachments 3 and so arranged to be held above the anode members 15, the attachments 3 being for example placed on the flanges 13 as shown in Figure 15 or secured as required. Each electrolyte guide member 5' is positioned in a circular sector defined by two neighbouring radial flanges 13 and an arc of the outer ring 13' as shown in Figure 15.
The arrangement of the electrolyte guide members 5' and the anode 10' can be moulded as units. This offers the advantage of avoiding mechanical joints and the risk of altering the properties of the materials of the electrolyte guide members 5' or the anode 10' by welding.
- 26 -The anodes 10' and electrolyte guide members 5' can be made of the same materials, in particular they can be made of a metallic body having an outer part with a layer containing predominantly CoO.
Figure 16 illustrates a square anode 10' as a variation of the round anode 10' of Figures 13 and 15.
The anode 10' of Figure 16 has generally rectangular concentric parallel anode members 15 with rounded corners. The anode 10' shown in Figure 16 can be fitted with electrolyte guide members similar to those of Figures 13 to 15 but in a corresponding rectangular arrangement.
The anodes 10' of Figures 13 and 16 can be made by casting a metal or an alloy. Typically, an anode substrate, for example consisting manly of nickel, can be cast to form the anode's internal structure which is then coated as described above to form the anode's outer part having a layer that consists predominantly of CoO.
Alternatively, cobalt or a cobalt alloy can be cast to form the anode's internal structure which is then oxidised as described above to form an outer part with a layer that consist predominantly of CoO. It is also contemplated to cast cobalt or a cobalt alloy around an anode core or skeleton having a different composition than the cast cobalt or cobalt alloy, for example iron or steel. The electrolyte guide members 5' can be manufactured by the same method and with the same or different materials.
Useful variations of this anode structure are disclosed in the abovementioned W000/40782. Further suitable anode designs are disclosed W099/027064 (de Nora/Duruz), W001/31088, W003/006716 and W003/023092 and US 5,368,702 (all de Nora) The manufacturing and behaviour in an aluminium electrowinning cell of the cobalt-oxide containing material used for the anode of the present invention will be further described in the following examples:
Comparative Example 1
Figure 16 illustrates a square anode 10' as a variation of the round anode 10' of Figures 13 and 15.
The anode 10' of Figure 16 has generally rectangular concentric parallel anode members 15 with rounded corners. The anode 10' shown in Figure 16 can be fitted with electrolyte guide members similar to those of Figures 13 to 15 but in a corresponding rectangular arrangement.
The anodes 10' of Figures 13 and 16 can be made by casting a metal or an alloy. Typically, an anode substrate, for example consisting manly of nickel, can be cast to form the anode's internal structure which is then coated as described above to form the anode's outer part having a layer that consists predominantly of CoO.
Alternatively, cobalt or a cobalt alloy can be cast to form the anode's internal structure which is then oxidised as described above to form an outer part with a layer that consist predominantly of CoO. It is also contemplated to cast cobalt or a cobalt alloy around an anode core or skeleton having a different composition than the cast cobalt or cobalt alloy, for example iron or steel. The electrolyte guide members 5' can be manufactured by the same method and with the same or different materials.
Useful variations of this anode structure are disclosed in the abovementioned W000/40782. Further suitable anode designs are disclosed W099/027064 (de Nora/Duruz), W001/31088, W003/006716 and W003/023092 and US 5,368,702 (all de Nora) The manufacturing and behaviour in an aluminium electrowinning cell of the cobalt-oxide containing material used for the anode of the present invention will be further described in the following examples:
Comparative Example 1
- 27 -A cylindrical metallic cobalt sample was oxidised to form an integral cobalt oxide layer that did not predominantly contain CoO. The cobalt samples contained no more than a total of 1 wt% additives and impurities and had a diameter of 1.94 cm and a height of 3 cm.
Oxidation was carried out by placing the cobalt sample into an oven in air and increasing the temperature from room temperature to 850 C at a rate of 120 C/hour.
After 24 hours at 850 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a greyish oxide scale having a thickness of about 300 micron. This oxide scale was made of: a 80 micron thick inner layer that had a porosity of 5% with pores that had a size of 2-5 micron; and a 220 micron thick outer layer having an open porosity of 20% with pores that had a size of 10-20 micron. The outer oxide layer was made of a mixture of essentially Co203 and Co304. The denser inner oxide layer was made of CoO.
As shown in Comparative Examples 2 and 3, such oxidised cobalt provides poor results when used as an anode material in an aluminium electrowinning cell.
Example la A cobalt sample which can be used to manufacture for an anode according to the invention was prepared as in Comparative Example 1 except that the sample was oxidised in an oven heated from room temperature to a temperature of 950 C (instead of 850 C) at the same rate (120 C/hour).
After 24 hours at 950 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a black glassy oxide scale having a thickness of about 350 micron (instead of 300 micron). This oxide scale had a continuous structure (instead of a layered structure)
Oxidation was carried out by placing the cobalt sample into an oven in air and increasing the temperature from room temperature to 850 C at a rate of 120 C/hour.
After 24 hours at 850 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a greyish oxide scale having a thickness of about 300 micron. This oxide scale was made of: a 80 micron thick inner layer that had a porosity of 5% with pores that had a size of 2-5 micron; and a 220 micron thick outer layer having an open porosity of 20% with pores that had a size of 10-20 micron. The outer oxide layer was made of a mixture of essentially Co203 and Co304. The denser inner oxide layer was made of CoO.
As shown in Comparative Examples 2 and 3, such oxidised cobalt provides poor results when used as an anode material in an aluminium electrowinning cell.
Example la A cobalt sample which can be used to manufacture for an anode according to the invention was prepared as in Comparative Example 1 except that the sample was oxidised in an oven heated from room temperature to a temperature of 950 C (instead of 850 C) at the same rate (120 C/hour).
After 24 hours at 950 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a black glassy oxide scale having a thickness of about 350 micron (instead of 300 micron). This oxide scale had a continuous structure (instead of a layered structure)
- 28 -with an open porosity of 10% (instead of 20%) and pores that had a size of 5 micron. The outer oxide layer was made of CoO produced above 895 C from the conversion into CoO of Co304 and glassy Co2O3 formed below this temperature and by oxidising the metallic outer part of the sample (underneath the cobalt oxide) directly into CoO. The porosity was due to the change of phase during the conversion of Co2O3 and Co3O4 to CoO.
Such a material can be used for making an aluminium electrowinning anode according to the invention. However, the density of the CoO layer and the performances of this material can be further improved as shown in Examples ic and id.
In general, to allow appropriate conversion of the cobalt oxide and growth of CoO from the metallic outer part of the substrate, it is important to leave the sample sufficiently long at a temperature above 895 C.
The length of the heat treatment will depend on the oxygen content of the oxidising atmosphere, the temperature of the heat treatment, the desired amount of CoO and the amount of Co2O3 and Co3O4 to convert into CoO.
Example lb Example la was repeated with a similar cylindrical metallic cobalt sample. The oven in which the sample was oxidised was heated to a temperature of 1050 C (instead of 950 C) at the same rate (120 C/hour).
After 24 hours at 1050 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a black crystallised oxide scale having a thickness of about 400 micron (instead of 350 micron) . This oxide scale had a continuous structure with an open porosity of 20%
(instead of 10%) and pores that had a size of 5 micron.
The outer oxide layer was made of CoO produced above 895 C like in Example la.
Such a oxidised cobalt is comparable to the oxidised cobalt of Example la and can likewise be used as an anode
Such a material can be used for making an aluminium electrowinning anode according to the invention. However, the density of the CoO layer and the performances of this material can be further improved as shown in Examples ic and id.
In general, to allow appropriate conversion of the cobalt oxide and growth of CoO from the metallic outer part of the substrate, it is important to leave the sample sufficiently long at a temperature above 895 C.
The length of the heat treatment will depend on the oxygen content of the oxidising atmosphere, the temperature of the heat treatment, the desired amount of CoO and the amount of Co2O3 and Co3O4 to convert into CoO.
Example lb Example la was repeated with a similar cylindrical metallic cobalt sample. The oven in which the sample was oxidised was heated to a temperature of 1050 C (instead of 950 C) at the same rate (120 C/hour).
After 24 hours at 1050 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a black crystallised oxide scale having a thickness of about 400 micron (instead of 350 micron) . This oxide scale had a continuous structure with an open porosity of 20%
(instead of 10%) and pores that had a size of 5 micron.
The outer oxide layer was made of CoO produced above 895 C like in Example la.
Such a oxidised cobalt is comparable to the oxidised cobalt of Example la and can likewise be used as an anode
- 29 -material to produce aluminium according to the present invention.
In general, to allow appropriate conversion of the cobalt oxide and growth of CoO from the metallic outer part of the substrate, it is important to leave the sample sufficiently long at a temperature above 895 C.
The length of the heat treatment above 895 C will depend on the oxygen content of the oxidising atmosphere, the temperature of the heat treatment, the desired amount of CoO and the amount of Co203 and Co304 (produced below 895 C) which needs to be converted into CoO.
Example lc (improved material) Example la was repeated with a similar cylindrical metallic cobalt sample. The oven in which the sample was .oxidised was heated to the same temperature (950 C) at a rate of 360 C/hour (instead of 120 C/hour).
After 24 hours at 950 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a dark grey substantially non-glassy oxide scale having a thickness of about 350 micron. This oxide scale had a continuous structure with an open porosity of less than 5% (instead of 10%) and pores that had a size of 5 micron.
The outer oxide layer was made of CoO that was formed directly from metallic cobalt above 895 C which was reached after about 2.5 hours and to a limited extent from the conversion of previously formed Co2O3 and Co3O4.
It followed that there was less porosity caused by the conversion of Co2O3 and Co304 to CoO than in Example la.
Such an oxidised cobalt sample has a significantly higher density than the samples of Examples la and lb, and is substantially crack-free. This oxidised cobalt constitutes a preferred material for making an improved aluminium electrowinning anode for use in a cell according to the invention.
In general, to allow appropriate conversion of the cobalt oxide and growth of CoO from the metallic outer part of the substrate, it is important to leave the sample sufficiently long at a temperature above 895 C.
The length of the heat treatment above 895 C will depend on the oxygen content of the oxidising atmosphere, the temperature of the heat treatment, the desired amount of CoO and the amount of Co203 and Co304 (produced below 895 C) which needs to be converted into CoO.
Example lc (improved material) Example la was repeated with a similar cylindrical metallic cobalt sample. The oven in which the sample was .oxidised was heated to the same temperature (950 C) at a rate of 360 C/hour (instead of 120 C/hour).
After 24 hours at 950 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a dark grey substantially non-glassy oxide scale having a thickness of about 350 micron. This oxide scale had a continuous structure with an open porosity of less than 5% (instead of 10%) and pores that had a size of 5 micron.
The outer oxide layer was made of CoO that was formed directly from metallic cobalt above 895 C which was reached after about 2.5 hours and to a limited extent from the conversion of previously formed Co2O3 and Co3O4.
It followed that there was less porosity caused by the conversion of Co2O3 and Co304 to CoO than in Example la.
Such an oxidised cobalt sample has a significantly higher density than the samples of Examples la and lb, and is substantially crack-free. This oxidised cobalt constitutes a preferred material for making an improved aluminium electrowinning anode for use in a cell according to the invention.
- 30 -Example id (improved material) Example lc was repeated with a similar cylindrical metallic cobalt sample. The oven in which the sample was oxidised was heated to the same temperature (1050 C) at a rate of 600 C/hour (instead of 120 C/hour in Example la and lb and 360 C/hour in Example ic).
After 18 hours at 1050 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a dark grey substantially non-glassy oxide scale having a thickness of about 300 micron (instead of 400 micron in Example lb and 350 micron in Example lc). This oxide scale had a continuous structure with a crack-free open porosity of less than 5% (instead of 20% in Example lb) and pores that had a size of less than 2 micron (instead of 5 micron in Example lb and in Example lc).
The outer oxide layer was made of CoO that was formed directly from metallic cobalt above 895 C which was reached after about 1.5 hours and to a marginal extent from the conversion of previously formed Co203 and Co304. It followed that there was significantly less porosity caused by the conversion of Co203 and Co304 to CoO than in Example lb and in Example lc.
Such an oxidised cobalt sample has a significantly higher density than the samples of Examples la and lb, and is substantially crack-free. This oxidised cobalt constitutes a preferred material for making an improved aluminium electrowinning anode according to the invention.
Comparative Example 2 (overpotential testing) An anode made of metallic cobalt oxidised under the conditions of Comparative Example 1 was tested in an aluminium electrowinning cell.
The cell's electrolyte was at a temperature of 925 C
and made of 11 wt% A1F3, 4 wt% CaF2, 7 wt% KF and 9.6 wt%
A1203, the balance being cryolite Na3AlF6.
After 18 hours at 1050 C, the oxidised cobalt sample was allowed to cool down to room temperature and examined.
The cobalt sample was covered with a dark grey substantially non-glassy oxide scale having a thickness of about 300 micron (instead of 400 micron in Example lb and 350 micron in Example lc). This oxide scale had a continuous structure with a crack-free open porosity of less than 5% (instead of 20% in Example lb) and pores that had a size of less than 2 micron (instead of 5 micron in Example lb and in Example lc).
The outer oxide layer was made of CoO that was formed directly from metallic cobalt above 895 C which was reached after about 1.5 hours and to a marginal extent from the conversion of previously formed Co203 and Co304. It followed that there was significantly less porosity caused by the conversion of Co203 and Co304 to CoO than in Example lb and in Example lc.
Such an oxidised cobalt sample has a significantly higher density than the samples of Examples la and lb, and is substantially crack-free. This oxidised cobalt constitutes a preferred material for making an improved aluminium electrowinning anode according to the invention.
Comparative Example 2 (overpotential testing) An anode made of metallic cobalt oxidised under the conditions of Comparative Example 1 was tested in an aluminium electrowinning cell.
The cell's electrolyte was at a temperature of 925 C
and made of 11 wt% A1F3, 4 wt% CaF2, 7 wt% KF and 9.6 wt%
A1203, the balance being cryolite Na3AlF6.
- 31 -The anode was placed in the cell's electrolyte at a distance of 4 cm from a facing cathode. An electrolysis current of 7.3 A was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The electrolysis current was varied between 4 and 10 A and the corresponding cell voltage measured to estimate the oxygen overpotential at the anode.
By extrapolating the cell's potential at a zero electrolysis current, it was found that the oxygen overpotential at the anode was of 0.88 V.
Example 2 (overpotential testing) A test was carried out under the conditions of Comparative Example 2 with two anodes made of metallic cobalt oxidised under the conditions of Example lc and id, respectively, in cells according to the invention using the same electrolyte as in Comparative Example 2.
The estimated oxygen overpotential for these anodes were at 0.22 V and 0.21 V, respectively, i.e. about 75% lower than in Comparative Example 2.
It follows that the use of metallic cobalt covered with an integral layer of CoO instead of Co203 and Co304 as an aluminium electrowinning anode material in a cell according to the invention leads to a significant saving of energy.
Comparative Example 3 (aluminium electrowinning) Another anode made of metallic cobalt oxidised under the conditions of Comparative Example 1, i.e. resulting in a Co203 and Co304 integral surface layer, was tested in an aluminium electrowinning cell. The cell's electrolyte was at 925 C and had the same composition as in Comparative Example 2. A nominal electrolysis current of 7.3 A was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage at start-up was above 20 V and dropped to 5.6 V after about 30 seconds. During the
The electrolysis current was varied between 4 and 10 A and the corresponding cell voltage measured to estimate the oxygen overpotential at the anode.
By extrapolating the cell's potential at a zero electrolysis current, it was found that the oxygen overpotential at the anode was of 0.88 V.
Example 2 (overpotential testing) A test was carried out under the conditions of Comparative Example 2 with two anodes made of metallic cobalt oxidised under the conditions of Example lc and id, respectively, in cells according to the invention using the same electrolyte as in Comparative Example 2.
The estimated oxygen overpotential for these anodes were at 0.22 V and 0.21 V, respectively, i.e. about 75% lower than in Comparative Example 2.
It follows that the use of metallic cobalt covered with an integral layer of CoO instead of Co203 and Co304 as an aluminium electrowinning anode material in a cell according to the invention leads to a significant saving of energy.
Comparative Example 3 (aluminium electrowinning) Another anode made of metallic cobalt oxidised under the conditions of Comparative Example 1, i.e. resulting in a Co203 and Co304 integral surface layer, was tested in an aluminium electrowinning cell. The cell's electrolyte was at 925 C and had the same composition as in Comparative Example 2. A nominal electrolysis current of 7.3 A was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage at start-up was above 20 V and dropped to 5.6 V after about 30 seconds. During the
- 32 -initial 5 hours, the cell voltage fluctuated about 5.6 V
between 4.8 and 6.4 V with short peaks above 8 V. After this initial period, the cell voltage stabilised at 4.0-4.2 V.
Throughout electrolysis, fresh alumina was fed to the electrolyte to compensate for the electrolysed alumina.
After 100 hours electrolysis, the anode was removed from the cell, allowed to cool down to room temperature and examined.
The anode's diameter had increased from 1.94 to 1.97 cm. The anode's metallic part had been heavily oxidised.
The thickness of the integral oxide scale had increased from 350 micron to about 1.1-1.5 mm. The oxide scale was made of: a 300-400 micron thick outer layer containing pores having a size of 30-50 micron and having cracks; a 1-1.1 mm thick inner layer that had been formed-during electrolysis. The inner layer was porous and contained electrolyte under the cracks of the outer layer.
Example 3 (aluminium electrowinning) An anode made of metallic cobalt oxidised under the conditions of Example lc, i.e. resulting in a CoO
integral surface layer was tested in an aluminium electrowinning cell under the conditions of Comparative Example 3. A nominal electrolysis current of 7.3 A was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
At start-up the cell voltage was 4.1 V and steadily decreased to 3.7-3.8 V after 30 minutes (instead of 4-4.2 in Comparative Example 3). The cell voltage stabilised at this level throughout the test without noticeable fluctuations, unlike in Comparative Example 3.
After 100 hours electrolysis, the anode was removed from the cell, allowed to cool down to room temperature and examined.
The anode's external diameter did not change during electrolysis and remained at 1.94 cm. The metallic cobalt
between 4.8 and 6.4 V with short peaks above 8 V. After this initial period, the cell voltage stabilised at 4.0-4.2 V.
Throughout electrolysis, fresh alumina was fed to the electrolyte to compensate for the electrolysed alumina.
After 100 hours electrolysis, the anode was removed from the cell, allowed to cool down to room temperature and examined.
The anode's diameter had increased from 1.94 to 1.97 cm. The anode's metallic part had been heavily oxidised.
The thickness of the integral oxide scale had increased from 350 micron to about 1.1-1.5 mm. The oxide scale was made of: a 300-400 micron thick outer layer containing pores having a size of 30-50 micron and having cracks; a 1-1.1 mm thick inner layer that had been formed-during electrolysis. The inner layer was porous and contained electrolyte under the cracks of the outer layer.
Example 3 (aluminium electrowinning) An anode made of metallic cobalt oxidised under the conditions of Example lc, i.e. resulting in a CoO
integral surface layer was tested in an aluminium electrowinning cell under the conditions of Comparative Example 3. A nominal electrolysis current of 7.3 A was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
At start-up the cell voltage was 4.1 V and steadily decreased to 3.7-3.8 V after 30 minutes (instead of 4-4.2 in Comparative Example 3). The cell voltage stabilised at this level throughout the test without noticeable fluctuations, unlike in Comparative Example 3.
After 100 hours electrolysis, the anode was removed from the cell, allowed to cool down to room temperature and examined.
The anode's external diameter did not change during electrolysis and remained at 1.94 cm. The metallic cobalt
- 33 -.inner part underneath the oxide scale had slightly decreased from 1.85 to 1.78 cm. The thickness of the cobalt oxide scale had increased from 0.3 to 0.7-0.8 mm (instead of 1-1.1 mm of Comparative Example 3) and was made of: a non-porous 300-400 micron thick external layer; and a porous 400 micron thick internal layer that had been formed during electrolysis. This internal oxide growth (400 micron thickness over 100 hours) was much less than the growth observed in Comparative example 3 (1-1.1 mm thickness over 100 hours).
It follows that the anode's CoO integral surface layer inhibits diffusion of oxygen and oxidation of the underlying metallic cobalt, compared to the CoZ03 and Co304 integral surface layer of the anode of Comparative Example 3.
Example 4 (Variations) The anode material of Examples la to ld, 2 and 3 can be covered upon formation of the integral CoO layer with a slurry applied layer, in particular containing CoFe2O4 particulate in a iron hydroxide colloid followed by drying at 250 C to form a protective layer on the CoO
integral layer.
Example 5 A coated anode for use in a cell according to the invention was made by covering a metallic cobalt substrate with an applied electrochemically active coating comprising an outer CoO layer and an inner layer of tantalum and cobalt oxides.
The coating was formed by applying cobalt and tantalum using electrodeposition. Specifically, tantalum was dispersed in the form of physical inclusions in cobalt electrodeposits.
The electrodeposition bath had a pH of 3.0 to 3.5 and contained:
- 400 g/l CoSO4.7H2O;
- 40 g/1 H3BO3;
- 40 g/1 KC1; and
It follows that the anode's CoO integral surface layer inhibits diffusion of oxygen and oxidation of the underlying metallic cobalt, compared to the CoZ03 and Co304 integral surface layer of the anode of Comparative Example 3.
Example 4 (Variations) The anode material of Examples la to ld, 2 and 3 can be covered upon formation of the integral CoO layer with a slurry applied layer, in particular containing CoFe2O4 particulate in a iron hydroxide colloid followed by drying at 250 C to form a protective layer on the CoO
integral layer.
Example 5 A coated anode for use in a cell according to the invention was made by covering a metallic cobalt substrate with an applied electrochemically active coating comprising an outer CoO layer and an inner layer of tantalum and cobalt oxides.
The coating was formed by applying cobalt and tantalum using electrodeposition. Specifically, tantalum was dispersed in the form of physical inclusions in cobalt electrodeposits.
The electrodeposition bath had a pH of 3.0 to 3.5 and contained:
- 400 g/l CoSO4.7H2O;
- 40 g/1 H3BO3;
- 40 g/1 KC1; and
- 34 -- 7-10 g/l Ta particles.
The tantalum particles had a size below 10 micron and were dispersed in the electrodeposition bath.
Electrodeposition on the cobalt substrate was carried out at a current density of 35 mA/cm2 which led to a cobalt deposit containing Ta inclusions, the deposit growing at a rate of 45 micron per hour on the substrate.
After the deposit had reached a total thickness of 250-300 micron, electrodeposition was interrupted. The deposit contained 9-15 wt% Ta corresponding to a volume fraction of 4-7 v%.
To form a coating, the substrate with its deposit were exposed to an oxidation treatment at a temperature of 950 C. The substrate with its deposit were brought from room temperature to 950 C at a rate of 450-500 C/hour in an oven to optimise the formation of Co0 instead of Co203 or Co304.
After 8 hours at 950 C, the substrate and the coating that was formed by oxidation of the deposit were taken out of the oven and allowed to cool down to room temperature. The coating had an outer oxide layer CoO on an inner oxide layer of Co-Ta oxides, in particular CoTaO41 that had grown from the deposit. The innermost part of the deposit had remained unoxidised, so that the Co-Ta oxide layer was integral with the remaining metallic Co-Ta deposit. The Co-Ta oxide layer and the CoO
layer had a total thickness of about 200 micron on the remaining metallic Co-Ta.
As demonstrated in Example 6, this CoO outer layer can act as an electrochemically active anode surface. The inner Co-Ta oxide layer inhibits oxygen diffusion towards the metallic cobalt substrate.
Example 6 A coated anode was made of a cobalt substrate covered with a Co-Ta coating as in Example 5 and used in a cell for the electrowinning aluminium according to the invention.
The tantalum particles had a size below 10 micron and were dispersed in the electrodeposition bath.
Electrodeposition on the cobalt substrate was carried out at a current density of 35 mA/cm2 which led to a cobalt deposit containing Ta inclusions, the deposit growing at a rate of 45 micron per hour on the substrate.
After the deposit had reached a total thickness of 250-300 micron, electrodeposition was interrupted. The deposit contained 9-15 wt% Ta corresponding to a volume fraction of 4-7 v%.
To form a coating, the substrate with its deposit were exposed to an oxidation treatment at a temperature of 950 C. The substrate with its deposit were brought from room temperature to 950 C at a rate of 450-500 C/hour in an oven to optimise the formation of Co0 instead of Co203 or Co304.
After 8 hours at 950 C, the substrate and the coating that was formed by oxidation of the deposit were taken out of the oven and allowed to cool down to room temperature. The coating had an outer oxide layer CoO on an inner oxide layer of Co-Ta oxides, in particular CoTaO41 that had grown from the deposit. The innermost part of the deposit had remained unoxidised, so that the Co-Ta oxide layer was integral with the remaining metallic Co-Ta deposit. The Co-Ta oxide layer and the CoO
layer had a total thickness of about 200 micron on the remaining metallic Co-Ta.
As demonstrated in Example 6, this CoO outer layer can act as an electrochemically active anode surface. The inner Co-Ta oxide layer inhibits oxygen diffusion towards the metallic cobalt substrate.
Example 6 A coated anode was made of a cobalt substrate covered with a Co-Ta coating as in Example 5 and used in a cell for the electrowinning aluminium according to the invention.
- 35 -The anode was suspended in the cell's electrolyte at a distance of 4 cm from a facing cathode. The electrolyte contained 11 wt% AlF3, 4 wt% CaF2, 7 wt% KF and 9.6 wt o A1203, the balance being Na3AlF6. The electrolyte was at a temperature of 925 C.
An electrolysis current was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage remained remarkably stable at 3.6 V
throughout electrolysis.
After 150 hours electrolysis, the anode was removed from the cell. No significant change of the anode's dimensions was observed by visual examination.
Example 7 Example 5 was repeated by applying a Co-Ta coating onto an anode substrate made of a metallic alloy containing 75 wt% Ni, 15 wt% Fe and 10 wt% Cu.
The anode was tested as in Example 6 at an anodic current density of 0.8 A/cm2. At start-up, the cell voltage was at 4.2 V and decreased within the first 24 hours to 3.7 V and remained stable thereafter.
After 120 hours electrolysis, the anode was removed from the cell. No sign of passivation of the nickel-rich substrate was observed and no significant change of dimensions of the anode was noticed by visual examination of the anode.
Example 8 Examples 5 to 7 can be repeated by substituting tantalum with niobium.
Example 9 Another anode for use in a cell according to the invention was made by applying a coating of Co-W onto an anode substrate made of a metallic alloy containing 75 wt% Ni, 15 wt% Fe and 10 wt% Cu.
An electrolysis current was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage remained remarkably stable at 3.6 V
throughout electrolysis.
After 150 hours electrolysis, the anode was removed from the cell. No significant change of the anode's dimensions was observed by visual examination.
Example 7 Example 5 was repeated by applying a Co-Ta coating onto an anode substrate made of a metallic alloy containing 75 wt% Ni, 15 wt% Fe and 10 wt% Cu.
The anode was tested as in Example 6 at an anodic current density of 0.8 A/cm2. At start-up, the cell voltage was at 4.2 V and decreased within the first 24 hours to 3.7 V and remained stable thereafter.
After 120 hours electrolysis, the anode was removed from the cell. No sign of passivation of the nickel-rich substrate was observed and no significant change of dimensions of the anode was noticed by visual examination of the anode.
Example 8 Examples 5 to 7 can be repeated by substituting tantalum with niobium.
Example 9 Another anode for use in a cell according to the invention was made by applying a coating of Co-W onto an anode substrate made of a metallic alloy containing 75 wt% Ni, 15 wt% Fe and 10 wt% Cu.
- 36 -The coating was formed by applying cobalt and tungsten using electrodeposition. The electrodeposition bath contained:
- 100 g/l CoC12.6H20;
- 45 g/l Na2WO4.2H20;
- 400 g/l KNaC4H4O6.4H20; and - 50 g/1 NH4C1.
Moreover, NH4OH had been added to this bath so that the bath had reached a pH of 8.5-8.7.
Electrodeposition on the Ni-Fe-Cu substrate was carried out at a temperature of 82-90 C and at a current density of 50 mA/cm2 which led to a cobalt-tungsten alloy deposit on the substrate, the deposit growing at a rate of 35-40 micron per hour at a cathodic current efficiency of about 90%.
After the deposit had reached a total thickness of about 250 micron, electrodeposition was interrupted. The deposited cobalt alloy contained 20-25 wt% tungsten.
To form a coating, the substrate with its deposit were exposed to an oxidation treatment at a temperature of 950 C. The substrate with its deposit were brought from room temperature to 950 C at a rate of 450-500 C/hour in an oven to optimise the formation of CoO
instead of Co203 or Co3O4.
After 8 hours at 950 C, the substrate and the coating that was formed by oxidation of the deposit were taken out of the oven and allowed to cool down to room temperature. The coating contained at its surface cobalt monoxide and tungsten oxide.
The structure of the coating after oxidation was denser and more coherent than the coating obtained by oxidising an electrodeposited layer of Ta-Co as disclosed in Example 1.
As demonstrated in Example 10, this coating can act as an electrochemically active anode surface. The presence of tungsten inhibits oxygen diffusion towards the metallic cobalt substrate.
- 100 g/l CoC12.6H20;
- 45 g/l Na2WO4.2H20;
- 400 g/l KNaC4H4O6.4H20; and - 50 g/1 NH4C1.
Moreover, NH4OH had been added to this bath so that the bath had reached a pH of 8.5-8.7.
Electrodeposition on the Ni-Fe-Cu substrate was carried out at a temperature of 82-90 C and at a current density of 50 mA/cm2 which led to a cobalt-tungsten alloy deposit on the substrate, the deposit growing at a rate of 35-40 micron per hour at a cathodic current efficiency of about 90%.
After the deposit had reached a total thickness of about 250 micron, electrodeposition was interrupted. The deposited cobalt alloy contained 20-25 wt% tungsten.
To form a coating, the substrate with its deposit were exposed to an oxidation treatment at a temperature of 950 C. The substrate with its deposit were brought from room temperature to 950 C at a rate of 450-500 C/hour in an oven to optimise the formation of CoO
instead of Co203 or Co3O4.
After 8 hours at 950 C, the substrate and the coating that was formed by oxidation of the deposit were taken out of the oven and allowed to cool down to room temperature. The coating contained at its surface cobalt monoxide and tungsten oxide.
The structure of the coating after oxidation was denser and more coherent than the coating obtained by oxidising an electrodeposited layer of Ta-Co as disclosed in Example 1.
As demonstrated in Example 10, this coating can act as an electrochemically active anode surface. The presence of tungsten inhibits oxygen diffusion towards the metallic cobalt substrate.
- 37 -Example 10 An anode was made as in Example 9 and used in a cell for the electrowinning of aluminium according to the invention.
The anode was suspended in the cell's electrolyte at a distance of 4 cm from a facing cathode. The electrolyte contained 11 wt% AlF3, 4 wt% CaF2, 7 wt o KF and 9.6 wt%
A1203, the balance being Na3AlF6. The electrolyte was at a temperature of 925 C.
An electrolysis current was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage remained stable at 3.5-3.7 V throughout electrolysis. After 100 hours electrolysis, the anode was removed from the cell. No change of the anode's dimensions was observed by visual examination.
Example 11 Examples 9 and 10 can be repeated with an anode substrate made of cobalt, nickel or an alloy of 92 wt%
nickel and 8 wt% copper.
Comparative tests show that the use in a conventional cryolite-based electrolyte at 960 C of a metal-based anode having an electrochemically active outer part comprising a layer that contains predominantly cobalt oxide CoO, leads to accelerated oxidation of the anode and dissolution into the electrolyte of oxides of the anode, in particular CoO. Moreover, use of such an anode in an electrolyte at 910 -940 C without potassium fluoride leads to corrosion or passivation the anode.
These Examples demonstrate that a material having an outer part with a layer that contains predominantly cobalt oxide CoO as described above, provides an enhanced stability during use in an aluminium electrowinning cell and is therefore suitable to protect anodes having a flow-through structure which is exposed to the fluoride-based molten electrolyte that is rendered more aggressive to the anodes by its circulation through the anodes.
The anode was suspended in the cell's electrolyte at a distance of 4 cm from a facing cathode. The electrolyte contained 11 wt% AlF3, 4 wt% CaF2, 7 wt o KF and 9.6 wt%
A1203, the balance being Na3AlF6. The electrolyte was at a temperature of 925 C.
An electrolysis current was passed from the anode to the cathode at an anodic current density of 0.8 A/cm2.
The cell voltage remained stable at 3.5-3.7 V throughout electrolysis. After 100 hours electrolysis, the anode was removed from the cell. No change of the anode's dimensions was observed by visual examination.
Example 11 Examples 9 and 10 can be repeated with an anode substrate made of cobalt, nickel or an alloy of 92 wt%
nickel and 8 wt% copper.
Comparative tests show that the use in a conventional cryolite-based electrolyte at 960 C of a metal-based anode having an electrochemically active outer part comprising a layer that contains predominantly cobalt oxide CoO, leads to accelerated oxidation of the anode and dissolution into the electrolyte of oxides of the anode, in particular CoO. Moreover, use of such an anode in an electrolyte at 910 -940 C without potassium fluoride leads to corrosion or passivation the anode.
These Examples demonstrate that a material having an outer part with a layer that contains predominantly cobalt oxide CoO as described above, provides an enhanced stability during use in an aluminium electrowinning cell and is therefore suitable to protect anodes having a flow-through structure which is exposed to the fluoride-based molten electrolyte that is rendered more aggressive to the anodes by its circulation through the anodes.
Claims (51)
1. A cell for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte, comprising at least one non-carbon metal-based anode having an electrically conductive metallic structure that comprises an outer part with an electrochemically active anode surface on which, during electrolysis, oxygen is anodically evolved, and which is suspended in the electrolyte substantially parallel to a facing cathode, said metallic structure having one or more flow-through openings extending from the active anode surface through the metallic structure, said flow-through opening(s) being arranged for guiding a circulation of electrolyte driven by the fast escape of anodically evolved oxygen, wherein said outer part of the anode comprises a layer that contains predominantly cobalt oxide CoO.
2. The cell of claim 1, wherein the anode structure is a foraminate structure.
3. The cell of claim 2, wherein the anode structure comprises a series of horizontal anode members having electrochemically active surfaces in a generally coplanar arrangement to form said active anode surface, the anode members being spaced apart to form longitudinal flow-through openings for the circulation of electrolyte driven by the fast escape of anodically evolved oxygen.
4. The cell of claim 3, wherein the anode members are blades, bars, rods or wires.
5. The cell of any one of claims 1 to 4, wherein the active anode surface is substantially horizontal.
6. The cell of any one of claims 1 to 4, wherein the active anode surface is substantially vertical or inclined to the horizontal.
7. The cell of any one of claims 1 to 6, wherein the molten electrolyte is at a temperature in the range from 910° to 940°C, and consists of:
- 6.5 to 11 weight% dissolved alumina;
- 35 to 44 weight% aluminium fluoride;
- 38 to 46 weight% sodium fluoride;
- 2 to 15 weight% potassium fluoride;
- 0 to 5 weight% calcium fluoride; and - 0 to 5 weight% in total of one or more further constituents.
- 6.5 to 11 weight% dissolved alumina;
- 35 to 44 weight% aluminium fluoride;
- 38 to 46 weight% sodium fluoride;
- 2 to 15 weight% potassium fluoride;
- 0 to 5 weight% calcium fluoride; and - 0 to 5 weight% in total of one or more further constituents.
8. The cell of claim 7, wherein the electrolyte contains as further constituent(s) at least one fluoride selected from magnesium fluoride, lithium fluoride, cesium fluoride, rubidium fluoride, strontium fluoride, barium fluoride and cerium fluoride.
9. The cell of any one of claims 1 to 8, wherein the electrolyte contains alumina at a concentration near saturation on the active anode surface.
10. The cell of any one of claims 1 to 9, wherein the CoO-containing layer is integral with a core made of cobalt or a cobalt alloy.
11. The cell of any one of claims 1 to 9, wherein the anode comprises an electrically conductive substrate that is covered with an applied electrochemically active coating that comprises the CoO-containing layer.
12. The cell of claim 11, wherein the CoO-containing layer is a layer of sintered particles.
13. The cell of claim 11, wherein the CoO-containing layer is an integral oxide layer on an applied Co-containing metallic layer of the coating.
14. The cell of any one of claims 11 to 13, which comprises an oxygen barrier layer between the CoO-containing layer and the electrically conductive substrate.
15. The cell of claim 14, wherein the oxygen barrier layer contains at least one metal selected from nickel, copper, tungsten, molybdenum, tantalum, niobium and chromium, or an oxide thereof.
16. The cell of claim 15, wherein the oxygen barrier layer further contains cobalt.
17. The cell of claim 16, wherein the oxygen barrier layer is a cobalt alloy containing at least one metal selected from nickel, tungsten, molybdenum, tantalum and niobium.
18. The cell of claim 17, wherein the cobalt alloy contains:
- at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wt%; and - one or more further elements and compounds in a total amount of up to 5 wt%, the balance being cobalt.
- at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wt%; and - one or more further elements and compounds in a total amount of up to 5 wt%, the balance being cobalt.
19. The cell of claim 18, containing as said further elements at least one of aluminium, silicon and manganese.
20. The cell of any one of claims 14 to 19, wherein the CoO-containing layer is integral with the oxygen barrier layer.
21. The cell of any one of claims 14 to 19, wherein the oxygen barrier layer is integral with the electrically conductive substrate.
22. The cell of any one of claims 14 to 19, wherein the oxygen barrier layer and the CoO-containing layer, or precursors thereof, are distinct applied layers.
23. The cell of claim 13, or claim 21 or 22 when depending on claim 13, wherein the Co-containing metallic layer contains cobalt in an amount of at least 95 wt%.
24. The cell of any one of claims 13 to 23, wherein the Co-containing metallic layer contains at least one additive selected from silicon, manganese, nickel niobium, tantalum and aluminium in a total amount of 0.1 to 2 wt%.
25. The cell of any one of claims 11 to 24, wherein the electrically conductive substrate comprises at least one metal selected from chromium, cobalt, hafnium, iron, nickel, copper, platinum, silicon, tungsten, molybdenum, tantalum, niobium, titanium, tungsten, vanadium, yttrium and zirconium, or a compound thereof, or a combination thereof.
26. The cell of claim 25, wherein the electrically conductive substrate has an outer part made of cobalt or a cobalt-rich alloy to which the coating is applied.
27. The cell of claim 26, wherein the outer part is made of a cobalt-rich alloy containing at least one of nickel, tungsten, molybdenum, tantalum and niobium, said cobalt alloy containing:
- at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wt%; and - one or more further elements and compounds in a total amount of up to 5 wt%, the balance being cobalt.
- at least one of nickel, tungsten, molybdenum, tantalum and niobium in a total amount of 5 to 30 wt%; and - one or more further elements and compounds in a total amount of up to 5 wt%, the balance being cobalt.
28. The cell of any one of claims 11 to 27, wherein the electrically conductive substrate contains or consists essentially of one or more oxidation-resistant metals.
29. The cell of claim 28, wherein said one or more oxidation-resistant metals is/are selected from nickel, cobalt, chromium and niobium.
30. The cell of claim 25, wherein the electrically conductive substrate is an alloy of nickel, iron and copper containing: 65 to 85 weight% nickel; 5 to 25 weight% iron; 1 to 20 weight% copper; and 0 to 10 weight%
further constituents.
further constituents.
31. The cell of claim 10, wherein the core is made of the same material as: the oxygen barrier layer of any one of claims 16 to 19; the Co-containing metallic layer of claim 23 or 24; or the cobalt-rich alloy of claim 27.
32. The cell of any one of claims 1 to 31, wherein the CoO-containing layer has an open porosity of up to 12%.
33. The cell of any one of claims 1 to 32, wherein the CoO-containing layer has a porosity with an average pore size below 7 micron.
34. The cell of any one of claims 1 to 33, wherein the CoO-containing layer contains cobalt oxide CoO in an amount of at least 80 wt%.
35. The cell of any one of claims 1 to 34, wherein the CoO-containing layer is substantially free of Co2O3 and substantially free Of CO3O4.
36. The cell of any one of claims 1 to 35, wherein the CoO-containing layer is electrochemically active for the oxidation of oxygen ions and is uncovered or is covered with an electrolyte-pervious layer.
37. The cell of any one of claims 1 to 35, wherein the CoO-containing layer is covered with an applied protective layer.
38. The cell of claim 37, wherein the applied protective layer contains cobalt oxide.
39. The cell of claim 37 or 38, wherein the applied protective layer contains iron oxide.
40. The cell of claim 39, wherein the applied protective layer contains oxides of cobalt and of iron.
41. The cell of any one of claims 37 to 40, wherein the applied protective layer contains a cerium compound.
42. The cell of any one of claims 37 to 41, wherein the applied protective layer is electrochemically active for the oxidation of oxygen ions and is uncovered or is covered with an electrolyte pervious-layer.
43. The cell of any one of claims 1 to 42, which has an electrochemically active surface that contains at least one dopant, in particular at least one dopant selected from iridium, palladium, platinum, rhodium, ruthenium, silicon, tungsten, molybdenum, tantalum, niobium, tin or zinc metals, Mischmetal, metals of the Lanthanide series, as metals and compounds, and mixtures thereof.
44. The cell of claim 43, wherein the electrochemically active surface is made of an active material containing the dopant(s) in a total amount of 0.1 to 5 wt%.
45. The cell of any one of claims 1 to 44, comprising a cathode that has an aluminium-wettable surface.
46. The cell of claim 45, wherein the cathode has an aluminium-wettable coating that comprises a refractory boride and/or an aluminium-wetting oxide.
47. The cell of any one of claims 1 to 46, wherein the anode is suspended in the electrolyte by a stem having an outer part comprising a layer that contains predominantly cobalt oxide CoO.
48. A method of producing aluminium in a cell as defined in any one of claims 1 to 47, comprising passing an electric current through the or each active anode structure to its active anode surfaces as electronic current and through the electrolyte to the cathode as ionic current, thereby electrolysing the dissolved alumina to produce aluminium on the cathode(s) and oxygen on the active anode surface(s) which is released through said flow-through openings.
49. The method of claim 48, wherein oxygen ions are oxidised on the anode's layer that contains predominantly cobalt oxide CoO.
50. The method of claim 48 or 49, wherein oxygen ions are oxidised on an active layer applied to the anode's layer that contains predominantly cobalt oxide CoO.
51. A non-carbon metal-based anode for the electrowinning of aluminium from alumina dissolved in a fluoride-containing molten electrolyte, comprising an electrically conductive metallic structure that comprises an outer part with an electrochemically active anode surface on which oxygen is anodically evolved and which is suspended in the electrolyte substantially parallel to a facing cathode during use, said metallic structure having one or more flow-through openings extending from the active anode surface through the metallic structure, said flow-through opening(s) being arranged for guiding during use a circulation of electrolyte driven by the fast escape of anodically evolved oxygen, wherein said outer part of the anode comprises a layer that contains predominantly cobalt oxide CoO.
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JP4916040B1 (en) * | 2011-03-25 | 2012-04-11 | 学校法人同志社 | Electrolytic sampling anode and electrolytic sampling method using the anode |
RU2532200C2 (en) * | 2012-07-20 | 2014-10-27 | Анатолий Иванович Киселев | Method of obtaining of aluminium by electrolysis of cryolite-aluminuos melt using carbon oxide |
US10711359B2 (en) | 2013-08-19 | 2020-07-14 | United Company RUSAL Engineering and Technology Centre LLC | Iron-based anode for obtaining aluminum by the electrolysis of melts |
CN105132952B (en) * | 2015-08-26 | 2017-09-29 | 贵州理工学院 | It is a kind of to reduce the electrolyte system of perfluocarbon discharge capacity |
RU2698162C2 (en) | 2017-03-01 | 2019-08-22 | Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" | Perforated metal inert anode for aluminium production by molten electrolysis |
RU2758697C1 (en) * | 2020-12-23 | 2021-11-01 | Евгений Сергеевич Горланов | Method for electrolytic production of aluminium using solid electrodes |
Family Cites Families (13)
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US4142005A (en) * | 1976-02-27 | 1979-02-27 | The Dow Chemical Company | Process for preparing an electrode for electrolytic cell having a coating of a single metal spinel, Co3 O4 |
US4146438A (en) * | 1976-03-31 | 1979-03-27 | Diamond Shamrock Technologies S.A. | Sintered electrodes with electrocatalytic coating |
FI67576C (en) * | 1979-12-26 | 1985-04-10 | Asahi Chemical Ind | VAETEALSTRINGSELEKTROD |
US6372119B1 (en) * | 1997-06-26 | 2002-04-16 | Alcoa Inc. | Inert anode containing oxides of nickel iron and cobalt useful for the electrolytic production of metals |
US6217739B1 (en) * | 1997-06-26 | 2001-04-17 | Alcoa Inc. | Electrolytic production of high purity aluminum using inert anodes |
US6077415A (en) * | 1998-07-30 | 2000-06-20 | Moltech Invent S.A. | Multi-layer non-carbon metal-based anodes for aluminum production cells and method |
WO2000006803A1 (en) * | 1998-07-30 | 2000-02-10 | Moltech Invent S.A. | Nickel-iron alloy-based anodes for aluminium electrowinning cells |
DE69905913T2 (en) * | 1998-08-18 | 2003-12-18 | Moltech Invent S.A., Luxemburg/Luxembourg | BIPOLAR CELL WITH CARBON CATHODES FOR THE PRODUCTION OF ALUMINUM |
US6521116B2 (en) * | 1999-07-30 | 2003-02-18 | Moltech Invent S.A. | Cells for the electrowinning of aluminium having dimensionally stable metal-based anodes |
US6638412B2 (en) * | 2000-12-01 | 2003-10-28 | Moltech Invent S.A. | Prevention of dissolution of metal-based aluminium production anodes |
US20040231979A1 (en) * | 2001-07-13 | 2004-11-25 | Vittorio De Nora | Alloy-based anode structures for aluminium production |
CA2557957C (en) * | 2004-03-18 | 2012-05-15 | Moltech Invent S.A. | Non-carbon anodes |
CA2558969C (en) * | 2004-03-18 | 2012-05-15 | Moltech Invent S.A. | Non-carbon anodes with active coatings |
-
2005
- 2005-05-25 CA CA2567127A patent/CA2567127C/en not_active Expired - Fee Related
- 2005-05-25 WO PCT/IB2005/051718 patent/WO2005118916A2/en active Application Filing
- 2005-05-25 RU RU2006147308/02A patent/RU2374362C2/en active
- 2005-05-25 EP EP05746937A patent/EP1756334A2/en not_active Withdrawn
- 2005-05-25 AU AU2005250240A patent/AU2005250240B2/en not_active Ceased
- 2005-05-25 US US11/628,211 patent/US20110100834A1/en not_active Abandoned
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RU2374362C2 (en) | 2009-11-27 |
EP1756334A2 (en) | 2007-02-28 |
WO2005118916A2 (en) | 2005-12-15 |
WO2005118916A3 (en) | 2007-03-15 |
AU2005250240A1 (en) | 2005-12-15 |
US20110100834A1 (en) | 2011-05-05 |
CA2567127A1 (en) | 2005-12-15 |
RU2006147308A (en) | 2008-07-20 |
AU2005250240B2 (en) | 2011-06-30 |
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