NO131845B - - Google Patents
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- NO131845B NO131845B NO1915/72A NO191572A NO131845B NO 131845 B NO131845 B NO 131845B NO 1915/72 A NO1915/72 A NO 1915/72A NO 191572 A NO191572 A NO 191572A NO 131845 B NO131845 B NO 131845B
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- Prior art keywords
- alloy
- magnesium
- silver
- gloss
- aluminum alloy
- Prior art date
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- 229910045601 alloy Inorganic materials 0.000 claims description 49
- 239000000956 alloy Substances 0.000 claims description 49
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 18
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 14
- 230000003647 oxidation Effects 0.000 claims description 14
- 238000007254 oxidation reaction Methods 0.000 claims description 14
- 238000005098 hot rolling Methods 0.000 claims description 13
- 229910052709 silver Inorganic materials 0.000 claims description 13
- 239000004332 silver Substances 0.000 claims description 13
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 12
- 229910052749 magnesium Inorganic materials 0.000 claims description 12
- 239000011777 magnesium Substances 0.000 claims description 12
- 229910000838 Al alloy Inorganic materials 0.000 claims description 10
- 238000007743 anodising Methods 0.000 claims description 10
- 229910052742 iron Inorganic materials 0.000 claims description 9
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 8
- 229910052710 silicon Inorganic materials 0.000 claims description 8
- 239000010703 silicon Substances 0.000 claims description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 7
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 6
- 229910052802 copper Inorganic materials 0.000 claims description 6
- 239000010949 copper Substances 0.000 claims description 6
- 238000000034 method Methods 0.000 claims description 6
- 239000010936 titanium Substances 0.000 claims description 6
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- 239000004411 aluminium Substances 0.000 claims description 5
- 230000009467 reduction Effects 0.000 claims description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 4
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 4
- 229910052804 chromium Inorganic materials 0.000 claims description 4
- 239000011651 chromium Substances 0.000 claims description 4
- 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 4
- 239000011701 zinc Substances 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 239000006104 solid solution Substances 0.000 claims description 3
- 238000005097 cold rolling Methods 0.000 claims 1
- QAOWNCQODCNURD-UHFFFAOYSA-N Sulfuric acid Chemical compound OS(O)(=O)=O QAOWNCQODCNURD-UHFFFAOYSA-N 0.000 description 10
- 230000007547 defect Effects 0.000 description 7
- 238000007598 dipping method Methods 0.000 description 7
- 238000002310 reflectometry Methods 0.000 description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 6
- 239000000395 magnesium oxide Substances 0.000 description 6
- CPLXHLVBOLITMK-UHFFFAOYSA-N magnesium oxide Inorganic materials [Mg]=O CPLXHLVBOLITMK-UHFFFAOYSA-N 0.000 description 6
- AXZKOIWUVFPNLO-UHFFFAOYSA-N magnesium;oxygen(2-) Chemical compound [O-2].[Mg+2] AXZKOIWUVFPNLO-UHFFFAOYSA-N 0.000 description 6
- 239000000243 solution Substances 0.000 description 6
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 4
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 4
- 238000010586 diagram Methods 0.000 description 4
- 229910017604 nitric acid Inorganic materials 0.000 description 4
- 229910000831 Steel Inorganic materials 0.000 description 3
- 229910021338 magnesium silicide Inorganic materials 0.000 description 3
- YTHCQFKNFVSQBC-UHFFFAOYSA-N magnesium silicide Chemical compound [Mg]=[Si]=[Mg] YTHCQFKNFVSQBC-UHFFFAOYSA-N 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 3
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- 229910000147 aluminium phosphate Inorganic materials 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 239000000047 product Substances 0.000 description 2
- 238000007789 sealing Methods 0.000 description 2
- 229910001369 Brass Inorganic materials 0.000 description 1
- 229910019142 PO4 Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- SNAAJJQQZSMGQD-UHFFFAOYSA-N aluminum magnesium Chemical compound [Mg].[Al] SNAAJJQQZSMGQD-UHFFFAOYSA-N 0.000 description 1
- 238000002048 anodisation reaction Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000009835 boiling Methods 0.000 description 1
- 239000010951 brass Substances 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 229910000397 disodium phosphate Inorganic materials 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- NBIIXXVUZAFLBC-UHFFFAOYSA-K phosphate Chemical compound [O-]P([O-])([O-])=O NBIIXXVUZAFLBC-UHFFFAOYSA-K 0.000 description 1
- 239000010452 phosphate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000035945 sensitivity Effects 0.000 description 1
- 239000010935 stainless steel Substances 0.000 description 1
- 229910001220 stainless steel Inorganic materials 0.000 description 1
- 230000004584 weight gain Effects 0.000 description 1
- 235000019786 weight gain Nutrition 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Metal Rolling (AREA)
- Laminated Bodies (AREA)
- Chemical Treatment Of Metals (AREA)
Description
Aluminiumlegeringer inneholdende 0,5 til 3% magnesium Aluminum alloys containing 0.5 to 3% magnesium
med små mengder av jern og silisium finner utstrakt anvendelse i teknikken, f.eks. for glansanodisert tilbehør for biler. De bear-beides vanligvis til plater, neddykkes i et glansbad, anodiseres i svovelsyre og tettes så at de får en glansfull, reflekterende, korrosjonsmotstandsdyktig ovarflate egnet for dekorative og mekaniske formål. Når de anvendes for bil-tilbehør, har disse glansanodiserte aluminiumlegeringer et utseende som ligner polert rustfritt stål eller kromplettert messing, men de er billigere for brukeren. with small amounts of iron and silicon find extensive use in technology, e.g. for gloss anodized accessories for cars. They are usually machined into sheets, immersed in a gloss bath, anodized in sulfuric acid and sealed to give a shiny, reflective, corrosion-resistant surface suitable for decorative and mechanical purposes. When used for automotive accessories, these bright anodized aluminum alloys have an appearance similar to polished stainless steel or chrome-plated brass, but are cheaper for the user.
Et av problemene forbundet med behandlingen av aluminium-magnesium-legeringer som skal glansanodiseres, er nødvendigheten av å holde magnesiumsilicidet i oppløsning under varmvalseprosessen. Dette er absolutt nødvendig for å oppnå et riktig resultat ved glans-behandlingen og anodiseringen i svovelsyre, slik at det oppnås en meget god speilrefleksjonsevne. For å holde magnesiumsilicidet i oppløsning under varmvalsingen, må man begynne valsingen ved used-vanlig høye temperaturer, mellom 450 og 525 °C, avhengig av legeringens magnesiuminnhold. Ved disse høye temperaturer avtar aluminium/ magnesium-legeringers oksydasjonsmotatand hurtig, og de rikelige mengder av løst vedheftende magnesiumoksyd blir dannet som en del av høytemperatur-oksydasjonsproduktet under varmvalsingen. Magne-siumoksydet kan enten hefte til valsene eller kan bli presset inn i den myke metalloverflate. Begge eventualiteter forårsaker over-flatedefekter som vanligvis betegnes som varmvalsingsfeil. Disse feil blir aldri fullstendig eliminert under den etterfølgende behandling, og de resulterer i defekter i den endelige glansanodiserte plate, hvilke defekter nedsetter speilrefleksjonsevnen og den senere korrosjonsmotstand. One of the problems associated with the treatment of aluminum-magnesium alloys to be bright anodized is the necessity to keep the magnesium silicide in solution during the hot rolling process. This is absolutely necessary to achieve a correct result with the gloss treatment and the anodizing in sulfuric acid, so that a very good specular reflection ability is achieved. In order to keep the magnesium silicide in solution during hot rolling, rolling must be started at unusually high temperatures, between 450 and 525 °C, depending on the alloy's magnesium content. At these high temperatures, the oxidation resistance of aluminium/magnesium alloys rapidly decreases, and the copious amounts of loosely adhering magnesium oxide are formed as part of the high temperature oxidation product during hot rolling. The magnesium oxide can either adhere to the rollers or can be pressed into the soft metal surface. Both eventualities cause surface defects commonly referred to as hot rolling defects. These defects are never completely eliminated during the subsequent processing, and they result in defects in the final gloss anodized plate, which defects reduce specular reflectivity and subsequent corrosion resistance.
Den foreliggende oppfinnelse tilveiebringer en aluminiumlegering med forbedret oksydasjonsmotstand ved høye temperaturer og som er egnet for glansanodisering, og legeringen er karakterisert ved at den består av 0,5 - 3% magnesium, 0,02 - 0,5% sølv, 0,001 - 0,2% jern, 0,001 *- 0,15% silisium, 0 - 0,10% kobber, 0 - 0,10% The present invention provides an aluminum alloy with improved oxidation resistance at high temperatures and which is suitable for bright anodizing, and the alloy is characterized in that it consists of 0.5 - 3% magnesium, 0.02 - 0.5% silver, 0.001 - 0, 2% iron, 0.001 *- 0.15% silicon, 0 - 0.10% copper, 0 - 0.10%
mangan, 0 - 0,10% sink, 0 - 0,05% krom og 0 - 0,05% titan, resten aluminium, og hvor sølvet vesentlig er i fast oppløsning i grunnmassen. Legeringens magnesiuminnhold er fortrinnsvis 0,8 - 2,8%. Legeringens sølvinnhold er fortrinnsvis 0,02 - 0,1%. manganese, 0 - 0.10% zinc, 0 - 0.05% chromium and 0 - 0.05% titanium, the rest aluminium, and where the silver is essentially in solid solution in the base mass. The alloy's magnesium content is preferably 0.8 - 2.8%. The silver content of the alloy is preferably 0.02 - 0.1%.
Oppfinnelsen omfatter også en fremgangsmåte til fremstilling av aluminiumlegeringer med forbedret oksydasjonsmotstand ved høye temperaturer og som er egnet for glansanodisering, og fremgangs- The invention also includes a method for producing aluminum alloys with improved oxidation resistance at high temperatures and which is suitable for bright anodizing, and progress
måten er karakterisert ved at the way is characterized by that
A) en legérirtg inneholdende 0,5 - 3% magnesium, 0,02 - 0,5% sølv, 0,001 - 0,2% jern, 0,001 - 0,15% silisium, 0 - 0,10% kobber, A) an alloy containing 0.5 - 3% magnesium, 0.02 - 0.5% silver, 0.001 - 0.2% iron, 0.001 - 0.15% silicon, 0 - 0.10% copper,
0 - 0,10% mangan, 0 - 0,10% sink, 0 - 0,005% krom og 0 - 0,05% titan og resten hovedsakelig aluminium holdes i minst 15 minutter 0 - 0.10% manganese, 0 - 0.10% zinc, 0 - 0.005% chromium and 0 - 0.05% titanium and the rest mainly aluminum is kept for at least 15 minutes
o o OE OE
innen temperaturomradet 450 - 525 C, within the temperature range 450 - 525 C,
B) Legeringen varmvalses med en begynnelsestemperatur i det under B) The alloy is hot-rolled with an initial temperature below that
A) angitte temperaturområde, A) specified temperature range,
C) Legeringen kaldtvalses og C) The alloy is cold rolled and
D) legeringen opphetes til temperaturområdet 175 - 400°C i 5 sek. til 8 timer. Foretrukne utførelsesformer er presisert i under-kravene. D) the alloy is heated to the temperature range 175 - 400°C for 5 sec. to 8 hours. Preferred embodiments are specified in the sub-claims.
Legeringen ifølge oppfinnelsen har mange fordeler. Den har en betydelig forbedret oksydasjonsmotstand i temperaturområdet 450 - 525°C, hvilket resulterer i bedre overflateutseende etter varmvalsingen. Legeringen tåler et bredere område av sammensetningen av den oppløsning i hvilken den behandles for oppnåelse av glans (glansdypping). Legeringen oppviser videre en betydelig øket glans etter anodisering i svovelsyre og påfølgende tetting av overflaten. The alloy according to the invention has many advantages. It has a significantly improved oxidation resistance in the temperature range 450 - 525°C, which results in a better surface appearance after hot rolling. The alloy tolerates a wider range of the composition of the solution in which it is treated to achieve gloss (gloss dipping). The alloy also shows a significantly increased shine after anodizing in sulfuric acid and subsequent sealing of the surface.
Det vises nå til tegningen: It now refers to the drawing:
Fig. 1 er et diagram som viser vektøkningen som funksjon av tiden når en sammenligningslegering A sammenlignes med legeringen B ifølge oppfinnelsen. Diagrammet og resultatene er omtalt i eksemplene. Fig. 2 er en kurve vedrørende ovennevnte legering A og legeringen B ifølge oppfinnelsen og viser potensialet som funksjon av konsentrasjonen av salpetersyre i glansdyppings-oppløsninger bestående av blandinger av salpetersyre og fosforsyre. Diagrammet og resultatene er omtalt i eksemplene. Fig. 1 is a diagram showing the increase in weight as a function of time when a comparison alloy A is compared with the alloy B according to the invention. The diagram and results are discussed in the examples. Fig. 2 is a curve relating to the above-mentioned alloy A and the alloy B according to the invention and shows the potential as a function of the concentration of nitric acid in gloss dipping solutions consisting of mixtures of nitric acid and phosphoric acid. The diagram and results are discussed in the examples.
Som nevnt ovenfor har legeringene ifølge oppfinnelsen As mentioned above, the alloys according to the invention have
en betydelig forbedret oksydasjonsmotstand ved temperaturer mellom 450 og 525°C, og de oppviser en mye bedre varmvalset overflate og refleksjonsevne etter glansdypping. Disse forbedrede overflateegenskaper blir oppnådd ved hjelp av legeringen og fremgangsmåten ifølge oppfinnelsen. Dessuten har legeringene ifølge oppfinnelsen gode mekaniske egenskaper og god bearbeidelsesevne. a significantly improved oxidation resistance at temperatures between 450 and 525°C, and they show a much better hot-rolled surface and reflectivity after gloss dipping. These improved surface properties are achieved by means of the alloy and the method according to the invention. In addition, the alloys according to the invention have good mechanical properties and good workability.
De fordelaktige overflateegenskaper som oppnås med legeringer ifølge oppfinnelsen, resulterer i meget mindre vrakgods som skyldes varmvalsedefekter under varmvalsingen ved høye temperaturer. Oksydasjonsproblemet lean ikke løses i konvensjonelle legeringer ved å nedsette varmvalsingstemperaturen og derved øke oksyda-sjonsmotstanden, fordi magnesiumsilicid da dannes i legeringens mikrostruktur og minsker følsomheten for glansbehandling og glansanodisering . The advantageous surface properties achieved with alloys according to the invention result in much less scrap due to hot rolling defects during hot rolling at high temperatures. The oxidation problem cannot be solved in conventional alloys by lowering the hot-rolling temperature and thereby increasing the oxidation resistance, because magnesium silicide is then formed in the microstructure of the alloy and reduces the sensitivity to gloss treatment and gloss anodization.
Legeringen ifølge oppfinnelsen hindrer ikke fullstendig dannelsen av nagnesiumoksyd som reaksjonsprodukt under opphetningen i temperaturområdet av 450 til 525°C. Imidlertid blir de mengder av magnesiumoksyd som dannes betydelig minsket, og det ser ut til at det fås en kompakt gjennomsiktig hinne som ikke blir fjernet fra metallet under varmvalsingen. Det er et overraskende trekk ved oppfinnelsen at syrekonsentrasjonsområdet i hvilket man kan oppnå en utmerket glans ved glansdyppingen, blir vesentlig utvidet med legeringer ifølge oppfinnelsen . Dermed blir andelen av uaksep-terbare produkter ved den etterfølgende glansdypping og anodisering betydelig minsket. Det er funnet at på grunn av d±. som er nevnt ovenfor, og takket være den forbedrede valsede overflate, blir glanstapet under anodiseringen i svovelsyre drastisk minsket. The alloy according to the invention does not completely prevent the formation of magnesium oxide as a reaction product during heating in the temperature range of 450 to 525°C. However, the amounts of magnesium oxide that are formed are significantly reduced, and it appears that a compact transparent film is obtained which is not removed from the metal during hot rolling. It is a surprising feature of the invention that the acid concentration range in which an excellent gloss can be achieved by gloss dipping is significantly expanded with alloys according to the invention. Thus, the proportion of unacceptable products in the subsequent gloss dipping and anodizing is significantly reduced. It is found that due to d±. as mentioned above, and thanks to the improved rolled surface, the loss of gloss during the anodizing in sulfuric acid is drastically reduced.
Som nevnt ovenfor inneholder legeringene 0,5 til 3% magnesium, 0,02 til 0,5% sølv, 0,001 til 0,2% jern, 0,001 til 0,15% silisium, resten vesentlig aluminium. Det foretrekkes at magnesiuminnholdet er fra 0,8 til 2,8% og sølvinnholdet fra 0,02 As mentioned above, the alloys contain 0.5 to 3% magnesium, 0.02 to 0.5% silver, 0.001 to 0.2% iron, 0.001 to 0.15% silicon, the remainder essentially aluminum. It is preferred that the magnesium content is from 0.8 to 2.8% and the silver content from 0.02
til 0,1%. Sølvet foreligger hovedsakelig i fast oppløsning i grunnmassen. to 0.1%. The silver is mainly present in solid solution in the base mass.
Fremgangsmåten ifølge oppfinnelsen beskrives kort i det følgende: Legeringen holdes ved en temperatur mellom 450 og 525°C The method according to the invention is briefly described in the following: The alloy is kept at a temperature between 450 and 525°C
i minst 15 minutter, idet den maksimale holdetid ikke er kritisk. Deretter blir legeringen varmvalset ved en begynnelsestemperatur innenfor de ovenfor nevnte temperaturgrenser og med en foretrukket tykkelsesreduksjon på minst 70%. Legeringen kan så kjøles fra varmvalsetemperaturen ved hjelp av hvilke som helst ønskede midler, f.eks. ved bråkjøling med vann. Legeringen blir deretter koldval- for at least 15 minutes, the maximum holding time not being critical. The alloy is then hot-rolled at an initial temperature within the above-mentioned temperature limits and with a preferred thickness reduction of at least 70%. The alloy can then be cooled from the hot rolling temperature by any desired means, e.g. by quenching with water. The alloy is then cold rolled
set til en foretrukket tykkelsesreduksjon på minst 50%, etterfulgt av en opphetning i 5 sekunder til 8 timer til et temperaturområde av 175°C til 400°C. set to a preferred thickness reduction of at least 50%, followed by heating for 5 seconds to 8 hours to a temperature range of 175°C to 400°C.
De følgende eksempler vil ytterligere belyse oppfinnelsen. The following examples will further illustrate the invention.
Eksempel I. Example I.
En sammenligningslegering A inneholdende 2,4% magnesium, 0,036% jern, 0,044% silisium, 0,041% kobber, 0,0088% titan, resten vesentlig aluminium, ble støpt som en kokilleblbkk med dimensjoner 7,5 cm x 17,5 cm x 105 cm. 3 mm ble høvlet bort fra hver overflate av blokken. Blokken ble forvarmet til 497°C og holdt ved denne temperatur i 8 timer, etterfulgt av valsing på polerte stålvalser med to suksessive tykkelsesreduksjoner på 20% og 30%. En betydelig mengde av oksyd ble overført på de polerte stålvalser, og overflaten av den varmvalsede legering var grov og diskontinuerlig. A comparison alloy A containing 2.4% magnesium, 0.036% iron, 0.044% silicon, 0.041% copper, 0.0088% titanium, the balance essentially aluminum, was cast as a mold blk with dimensions 7.5 cm x 17.5 cm x 105 cm. 3 mm was planed away from each surface of the block. The block was preheated to 497°C and held at this temperature for 8 hours, followed by rolling on polished steel rolls with two successive thickness reductions of 20% and 30%. A significant amount of oxide was transferred onto the polished steel rolls, and the surface of the hot-rolled alloy was rough and discontinuous.
Eksempel II Example II
En legering B inneholdende 2,5% magnesium, 0,05% sølv, 0,036% jern, 0,04.36 silisium, 0,045% kobber, 0,0089% titan, resten vesentlig aluminium, ble kokillestøpt, høvlet og varmvalset på samme måte som i eksempel I. De polerte stålvalser var vesent- An alloy B containing 2.5% magnesium, 0.05% silver, 0.036% iron, 0.04.36 silicon, 0.045% copper, 0.0089% titanium, the remainder essentially aluminium, was die cast, planed and hot rolled in the same manner as in example I. The polished steel rollers were essentially
lig frie for oksyd overført fra den hete aluminiumlegering, og den varmvalsede overflate var jern og fri for defekter. free from oxide transferred from the hot aluminum alloy, and the hot-rolled surface was iron and free from defects.
Eksempel III Example III
Legeringer A og B i eksemplene I og II ble opphetet til 497°C, holdt i 8 timer ved denne temperatur og varmvalset 10 gan-ger til en endelig tykkelse på 2,5 mm. Temperaturen etter den sis-te valsing var 370°C, og legeringene ble deretter bråkjølt i stille-stående vann. Legeringene ble deretter koldvalset til en tykkelse på 0,75 mm og ble delvis glødet ved 260°C i 2,5 timer. Etter denne behandling opptok overflaten av legeringen A en betydelig mengde magnesiumoksyd ved varmvalsing. På den annen side oppviste legeringen B ifølge oppfinnelsen en utmerket overflatejevnhet og var vesentlig fri for opptatt magnesiumoksyd. Alloys A and B in Examples I and II were heated to 497°C, held for 8 hours at this temperature and hot rolled 10 times to a final thickness of 2.5 mm. The temperature after the last rolling was 370°C, and the alloys were then quenched in still water. The alloys were then cold rolled to a thickness of 0.75 mm and partially annealed at 260°C for 2.5 hours. After this treatment, the surface of alloy A absorbed a significant amount of magnesium oxide during hot rolling. On the other hand, the alloy B according to the invention showed an excellent surface smoothness and was substantially free of occupied magnesium oxide.
Eksempel IV Example IV
Legeringer A og B behandlet i samsvar med eksempel III ble opphetet til 500°C i luft og holdt ved denne temperatur i 24 timer i hvilken tid man kontinuerlig registrerte vektøkningen ved okaydasjon ved hjelp av en registrerende mikrovekt. Resultatene er vist på fig. 1. Diagrammet viser klart at legeringen B ifølge oppfinnelsen har en betydelig minsket oksydasjonshastighet og oppviser i det vesentlige ingen oksydasjon i tiden mellom rundt 4 og 12 timer. I motsetning dertil hadde sammenligningslegeringen A en høy og konstant oksydasjonshastighet i dette tidsrom, og vektøk-ningskurven var vesentlig lineær. Alloys A and B treated in accordance with Example III were heated to 500°C in air and held at this temperature for 24 hours, during which time the increase in weight by oxidation was continuously recorded by means of a recording microbalance. The results are shown in fig. 1. The diagram clearly shows that the alloy B according to the invention has a significantly reduced oxidation rate and essentially shows no oxidation in the time between around 4 and 12 hours. In contrast, the comparison alloy A had a high and constant oxidation rate during this period, and the weight gain curve was essentially linear.
Eksempel V Example V
Legeringer A og B, behandlet i samsvar med eksempel III, ble behandlet i 120 sekunder i en oppløsning inneholdende 85% fosforsyre og forskjellige konsentrasjoner av en vandig 70%'s opp-løsning av salpetersyre, idet potensialet av prøven også ble målt. Badtemperaturen var 83°C. Resultatene, jfr. fig. 2, viser at en aksepterbar glansdypping ble oppnådd med legeringen B ifølge oppfinnelsen over et større område av salpetersyrekonsentrasjoner enn med sammenligningslegeringen A. Refleksjonsevnen til legeringen B ifølge oppfinnelsen etter glansdypping var 79%, idet et sølv- Alloys A and B, treated in accordance with Example III, were treated for 120 seconds in a solution containing 85% phosphoric acid and various concentrations of an aqueous 70% solution of nitric acid, the potential of the sample also being measured. The bath temperature was 83°C. The results, cf. fig. 2, shows that an acceptable gloss dip was achieved with the alloy B according to the invention over a larger range of nitric acid concentrations than with the comparison alloy A. The reflectivity of the alloy B according to the invention after gloss dipping was 79%, as a silver-
speil ble brukt som standard for 90% refleksjon. På den annen, side hadde legeringen A en refleksjonsevne på bare 58% etter glansdypping . mirror was used as standard for 90% reflection. On the other hand, alloy A had a reflectivity of only 58% after gloss dipping.
Eksempel VI Example VI
De glansdyppede prøver i eksempel V ble anodisert i The gloss-dipped samples in Example V were anodized in
20 minutter i 15%'s svovelsyre ved 25°C med en strømtetthet på 20 minutes in 15% sulfuric acid at 25°C with a current density of
220 A/m 2. Etter anodiseringen ble legeringene skylt og tettet i 10 minutter i kokende vann inneholdende 3 ppm fosfat tilsatt som Na2HP04> Refleksjonsevnen til legeringen B etter anodisering og tetting var 44 %, mens refleksjonsevnen til legeringen A bare var 34%, med et sølvspeil brukt som standard for en refleksjonsevne på 90% i begge tilfeller. 220 A/m 2. After anodizing, the alloys were rinsed and sealed for 10 minutes in boiling water containing 3 ppm phosphate added as Na2HP04> The reflectivity of alloy B after anodizing and sealing was 44%, while the reflectivity of alloy A was only 34%, with a silver mirror used as standard for a reflectivity of 90% in both cases.
Claims (7)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US14858271A | 1971-06-01 | 1971-06-01 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| NO131845B true NO131845B (en) | 1975-05-05 |
| NO131845C NO131845C (en) | 1975-08-13 |
Family
ID=22526397
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO1915/72A NO131845C (en) | 1971-06-01 | 1972-05-30 |
Country Status (7)
| Country | Link |
|---|---|
| US (1) | US3720508A (en) |
| CA (1) | CA959304A (en) |
| DE (1) | DE2226644C3 (en) |
| FR (1) | FR2141158A5 (en) |
| GB (1) | GB1379264A (en) |
| IT (1) | IT958105B (en) |
| NO (1) | NO131845C (en) |
Families Citing this family (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59193463A (en) * | 1983-04-18 | 1984-11-02 | Canon Inc | Photoconductive member |
| US4601796A (en) * | 1984-09-19 | 1986-07-22 | Aluminum Company Of America | High reflectance semi-specular anodized aluminum alloy product and method of forming same |
| JPS61201798A (en) * | 1985-03-01 | 1986-09-06 | Citizen Watch Co Ltd | Armor parts for wrist watch |
| US5032359A (en) * | 1987-08-10 | 1991-07-16 | Martin Marietta Corporation | Ultra high strength weldable aluminum-lithium alloys |
| US5122339A (en) * | 1987-08-10 | 1992-06-16 | Martin Marietta Corporation | Aluminum-lithium welding alloys |
| US5085830A (en) * | 1989-03-24 | 1992-02-04 | Comalco Aluminum Limited | Process for making aluminum-lithium alloys of high toughness |
| US5637404A (en) * | 1992-01-31 | 1997-06-10 | Aluminum Company Of America | Reflective aluminum strip |
| US5955147A (en) * | 1992-01-31 | 1999-09-21 | Aluminum Company Of America | Reflective aluminum trim |
| EP1997866A1 (en) * | 2007-05-22 | 2008-12-03 | Agfa HealthCare NV | Radiation image phosphor or scintillator panel |
| CN108893658A (en) * | 2018-07-11 | 2018-11-27 | 合肥华盖光伏科技有限公司 | A kind of high conductivity heat-resistant aluminum alloy wire and preparation method thereof |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US2586647A (en) * | 1946-02-08 | 1952-02-19 | Rolls Royce | Aluminum alloy |
| GB621617A (en) * | 1946-02-08 | 1949-04-13 | Harold Ernest Gresham | Aluminium alloy |
| US3306717A (en) * | 1964-02-01 | 1967-02-28 | Svenska Metallverken Ab | Filler metal for welding aluminumbased alloys |
-
1971
- 1971-06-01 US US00148582A patent/US3720508A/en not_active Expired - Lifetime
-
1972
- 1972-05-25 GB GB2476272A patent/GB1379264A/en not_active Expired
- 1972-05-26 IT IT50545/72A patent/IT958105B/en active
- 1972-05-30 NO NO1915/72A patent/NO131845C/no unknown
- 1972-05-31 CA CA143,818A patent/CA959304A/en not_active Expired
- 1972-05-31 DE DE2226644A patent/DE2226644C3/en not_active Expired
- 1972-06-01 FR FR7219774A patent/FR2141158A5/fr not_active Expired
Also Published As
| Publication number | Publication date |
|---|---|
| US3720508A (en) | 1973-03-13 |
| NO131845C (en) | 1975-08-13 |
| IT958105B (en) | 1973-10-20 |
| FR2141158A5 (en) | 1973-01-19 |
| DE2226644B2 (en) | 1980-07-17 |
| CA959304A (en) | 1974-12-17 |
| DE2226644C3 (en) | 1981-05-21 |
| GB1379264A (en) | 1975-01-02 |
| DE2226644A1 (en) | 1973-01-04 |
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