NO121038B - - Google Patents
Download PDFInfo
- Publication number
- NO121038B NO121038B NO16040365A NO16040365A NO121038B NO 121038 B NO121038 B NO 121038B NO 16040365 A NO16040365 A NO 16040365A NO 16040365 A NO16040365 A NO 16040365A NO 121038 B NO121038 B NO 121038B
- Authority
- NO
- Norway
- Prior art keywords
- uranium
- alloy
- temperature
- metal
- order
- Prior art date
Links
- 229910052770 Uranium Inorganic materials 0.000 claims description 22
- 229910045601 alloy Inorganic materials 0.000 claims description 21
- 239000000956 alloy Substances 0.000 claims description 21
- 229910052751 metal Inorganic materials 0.000 claims description 21
- JFALSRSLKYAFGM-UHFFFAOYSA-N uranium(0) Chemical compound [U] JFALSRSLKYAFGM-UHFFFAOYSA-N 0.000 claims description 21
- 239000002184 metal Substances 0.000 claims description 20
- 239000000463 material Substances 0.000 claims description 12
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims description 8
- 229910052726 zirconium Inorganic materials 0.000 claims description 8
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 238000000034 method Methods 0.000 claims description 5
- KDLHZDBZIXYQEI-UHFFFAOYSA-N Palladium Chemical compound [Pd] KDLHZDBZIXYQEI-UHFFFAOYSA-N 0.000 claims description 4
- 238000002844 melting Methods 0.000 claims description 4
- 230000008018 melting Effects 0.000 claims description 4
- 150000002739 metals Chemical class 0.000 claims description 4
- 239000000203 mixture Substances 0.000 claims description 4
- 230000003647 oxidation Effects 0.000 claims description 4
- 238000007254 oxidation reaction Methods 0.000 claims description 4
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims description 3
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 229910052804 chromium Inorganic materials 0.000 claims description 3
- 239000011651 chromium Substances 0.000 claims description 3
- 229910052750 molybdenum Inorganic materials 0.000 claims description 3
- 239000011733 molybdenum Substances 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 239000010936 titanium Substances 0.000 claims description 3
- 229910052720 vanadium Inorganic materials 0.000 claims description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 claims description 3
- KJTLSVCANCCWHF-UHFFFAOYSA-N Ruthenium Chemical compound [Ru] KJTLSVCANCCWHF-UHFFFAOYSA-N 0.000 claims description 2
- BQCADISMDOOEFD-UHFFFAOYSA-N Silver Chemical compound [Ag] BQCADISMDOOEFD-UHFFFAOYSA-N 0.000 claims description 2
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims description 2
- 239000004411 aluminium Substances 0.000 claims description 2
- 229910052787 antimony Inorganic materials 0.000 claims description 2
- WATWJIUSRGPENY-UHFFFAOYSA-N antimony atom Chemical compound [Sb] WATWJIUSRGPENY-UHFFFAOYSA-N 0.000 claims description 2
- 229910052793 cadmium Inorganic materials 0.000 claims description 2
- BDOSMKKIYDKNTQ-UHFFFAOYSA-N cadmium atom Chemical compound [Cd] BDOSMKKIYDKNTQ-UHFFFAOYSA-N 0.000 claims description 2
- 229910052738 indium Inorganic materials 0.000 claims description 2
- APFVFJFRJDLVQX-UHFFFAOYSA-N indium atom Chemical compound [In] APFVFJFRJDLVQX-UHFFFAOYSA-N 0.000 claims description 2
- 229910052758 niobium Inorganic materials 0.000 claims description 2
- 239000010955 niobium Substances 0.000 claims description 2
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims description 2
- 229910052763 palladium Inorganic materials 0.000 claims description 2
- 238000003303 reheating Methods 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
- 229910052709 silver Inorganic materials 0.000 claims description 2
- 239000004332 silver Substances 0.000 claims description 2
- 229910052718 tin Inorganic materials 0.000 claims description 2
- 229910052727 yttrium Inorganic materials 0.000 claims description 2
- VWQVUPCCIRVNHF-UHFFFAOYSA-N yttrium atom Chemical compound [Y] VWQVUPCCIRVNHF-UHFFFAOYSA-N 0.000 claims description 2
- 229910052845 zircon Inorganic materials 0.000 claims description 2
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 claims description 2
- 238000011282 treatment Methods 0.000 description 7
- 230000004992 fission Effects 0.000 description 6
- 238000010438 heat treatment Methods 0.000 description 5
- 239000012071 phase Substances 0.000 description 5
- 239000000654 additive Substances 0.000 description 4
- 230000000996 additive effect Effects 0.000 description 4
- 229910001093 Zr alloy Inorganic materials 0.000 description 2
- 238000005266 casting Methods 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 238000001556 precipitation Methods 0.000 description 2
- 230000035945 sensitivity Effects 0.000 description 2
- 238000007669 thermal treatment Methods 0.000 description 2
- NBWXXYPQEPQUSB-UHFFFAOYSA-N uranium zirconium Chemical class [Zr].[Zr].[U] NBWXXYPQEPQUSB-UHFFFAOYSA-N 0.000 description 2
- -1 0.1% by weight) Chemical compound 0.000 description 1
- OYPRJOBELJOOCE-UHFFFAOYSA-N Calcium Chemical compound [Ca] OYPRJOBELJOOCE-UHFFFAOYSA-N 0.000 description 1
- 229910000711 U alloy Inorganic materials 0.000 description 1
- 229910052791 calcium Inorganic materials 0.000 description 1
- 239000011575 calcium Substances 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000007872 degassing Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 230000004907 flux Effects 0.000 description 1
- 230000005484 gravity Effects 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 230000006698 induction Effects 0.000 description 1
- 150000002500 ions Chemical class 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 230000000877 morphologic effect Effects 0.000 description 1
- 230000000737 periodic effect Effects 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 230000008707 rearrangement Effects 0.000 description 1
- 230000009467 reduction Effects 0.000 description 1
- 239000011819 refractory material Substances 0.000 description 1
- 239000007790 solid phase Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 230000008646 thermal stress Effects 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- MZFRHHGRNOIMLW-UHFFFAOYSA-J uranium(4+);tetrafluoride Chemical compound F[U](F)(F)F MZFRHHGRNOIMLW-UHFFFAOYSA-J 0.000 description 1
- 238000005303 weighing Methods 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C07—ORGANIC CHEMISTRY
- C07D—HETEROCYCLIC COMPOUNDS
- C07D301/00—Preparation of oxiranes
- C07D301/02—Synthesis of the oxirane ring
- C07D301/03—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds
- C07D301/19—Synthesis of the oxirane ring by oxidation of unsaturated compounds, or of mixtures of unsaturated and saturated compounds with organic hydroperoxides
-
- C—CHEMISTRY; METALLURGY
- C07—ORGANIC CHEMISTRY
- C07C—ACYCLIC OR CARBOCYCLIC COMPOUNDS
- C07C39/00—Compounds having at least one hydroxy or O-metal group bound to a carbon atom of a six-membered aromatic ring
- C07C39/12—Compounds having at least one hydroxy or O-metal group bound to a carbon atom of a six-membered aromatic ring polycyclic with no unsaturation outside the aromatic rings
- C07C39/14—Compounds having at least one hydroxy or O-metal group bound to a carbon atom of a six-membered aromatic ring polycyclic with no unsaturation outside the aromatic rings with at least one hydroxy group on a condensed ring system containing two rings
-
- C—CHEMISTRY; METALLURGY
- C07—ORGANIC CHEMISTRY
- C07C—ACYCLIC OR CARBOCYCLIC COMPOUNDS
- C07C51/00—Preparation of carboxylic acids or their salts, halides or anhydrides
- C07C51/16—Preparation of carboxylic acids or their salts, halides or anhydrides by oxidation
- C07C51/31—Preparation of carboxylic acids or their salts, halides or anhydrides by oxidation of cyclic compounds with ring-splitting
- C07C51/313—Preparation of carboxylic acids or their salts, halides or anhydrides by oxidation of cyclic compounds with ring-splitting with molecular oxygen
Landscapes
- Chemical & Material Sciences (AREA)
- Organic Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Epoxy Compounds (AREA)
- Low-Molecular Organic Synthesis Reactions Using Catalysts (AREA)
- Catalysts (AREA)
- Manufacture And Refinement Of Metals (AREA)
Description
Fremgangsmåte til å fremstille et fisjonerbart materiale på uranbasis, særlig for reaktorer. Process for producing a fissionable uranium-based material, particularly for reactors.
Oppfinnelsen vedrører en fremgangsmåte til å fremstille et fisjonerbart materiale på uranbasis spesielt av den art som kan anvendes som fisjonsmaterialer i termiske reaktorer. The invention relates to a method for producing a fissionable uranium-based material, especially of the kind that can be used as fission materials in thermal reactors.
Formålet er i første rekke å oppnå at fisjonsmaterialet har god motstandsevne mot mekaniske påvirkninger, og mot termisk utmatning. The purpose is primarily to achieve that the fission material has good resistance to mechanical influences and to thermal exhaustion.
Oppfinnelsen vedrører altså en fremgangsmåte til å fremstille et fisjonerbart materiale på uranbasis inneholdende et av metallene aluminium, zirkon, krom, titan og vanadium med en mengde på 0,1—2 vekts-pst. av uranet, idet man smelter blandingen av nevnte metall med uran under vakuum ved temperatur av størrel-sesorden 1500° C, hvoretter man under betingelser som omtrent utelukker oksydasjon støper den smeltede legering i en vanlig støpeform og lar den støpte blokk av-kjøle, idet man holder den ved en temperatur over 1000° C, men under legeringens begynnende smeltetemperatur, og at man utsetter den gjenoppvarmede blokk for en avkjøling etterfulgt av en gjenoppvarm-ning til en temperatur av størrelsesorden 500—600° C, og fremgangsmåten er karakterisert ved at man for å nedsette behandlingstiden til nevnte blanding indirekte eller direkte setter et hjelpemetall som er forskjellig fra det førstnevnte og valgt blant metallene yttrium, zirkon, niob, molybden, rutenium, rodium, palladium, sølv, kadmium, indium, tinn, antimon i en mengde som utgjør 0,05—1 vekts-pst. av uranet. The invention therefore relates to a method for producing a fissionable uranium-based material containing one of the metals aluminium, zirconium, chromium, titanium and vanadium in an amount of 0.1-2% by weight. of the uranium, melting the mixture of said metal with uranium under vacuum at a temperature of the order of magnitude 1500° C, after which, under conditions which roughly exclude oxidation, the molten alloy is cast in an ordinary mold and the cast block is allowed to cool, it is kept at a temperature above 1000° C, but below the alloy's starting melting temperature, and that the reheated block is subjected to cooling followed by reheating to a temperature of the order of 500-600° C, and the method is characterized by in order to reduce the processing time of said mixture, indirectly or directly, an auxiliary metal which is different from the former and selected from among the metals yttrium, zircon, niobium, molybdenum, ruthenium, rhodium, palladium, silver, cadmium, indium, tin, antimony is added in an amount which amounts to 0.05-1% by weight. of the uranium.
Hjelpemetallet kan tilsettes i form av The auxiliary metal can be added in the form of
en legering med uran. an alloy with uranium.
Rent metallisk uran har anvendt som fisjonsmateriale i en termisk reaktor mekaniske ulemper som er desto større jo sterkere fluksen av nøytroner er jo sterkere den av reaktoren frembragte energi er. Fisjonsmaterialet i form av stenger eller staver blir deformert, og det er risiko for at de suksessive beskyttende omhyllinger blir ødelagt. Pure metallic uranium used as fission material in a thermal reactor has mechanical disadvantages which are greater the stronger the flux of neutrons, the stronger the energy produced by the reactor. The fission material in the form of rods or rods is deformed, and there is a risk that the successive protective sheaths are destroyed.
Det har derfor vist seg nødvendig å forandre strukturen av fisjonsmaterialet slik, at dette får en bedre motstandsevne mot termisk utmatning. It has therefore proved necessary to change the structure of the fission material so that it has a better resistance to thermal exhaustion.
Blant de hertil fremsatte forslag har det vist seg særlig fordelaktig å tilsette et metallisk element hvis kvalitet og mengde ikke har noen merkbar innflytelse på den normale drift av en termisk reaktor. Among the proposals put forward for this purpose, it has proven particularly advantageous to add a metallic element whose quality and quantity have no noticeable influence on the normal operation of a thermal reactor.
En slik tilsetning vil som regel vise seg i den erholdte legering i form av store korn som bevirker økt mekanisk svakhet på visse punkter i massen, hvorfor det for å eliminere dette er hensiktsmessig å un-derkaste massen en forlenget termisk behandling. Such an addition will usually appear in the resulting alloy in the form of large grains which cause increased mechanical weakness at certain points in the mass, which is why, to eliminate this, it is appropriate to subject the mass to an extended thermal treatment.
Den lange varighet av denne behandling vanskeliggjør og kompliserer den tek-niske fremstilling av fisjonerbare mate-rialer som består av slike legeringer. The long duration of this treatment makes the technical production of fissionable materials consisting of such alloys difficult and complicated.
Det ble i henhold til oppfinnelsen fun-net at en tilsetning av et annet hjelpeme-tallelement bevirker at det første metall-element oppløses hurtigere i fisjonsmaterialet, hvorfor hastigheten av den oven-nevnte termiske behandling som var fra 200—300 timer med et enkelt tilsetnings-element, nedsettes med minst 50 timer når det anvendes to tilsetningselementer. According to the invention, it was found that an addition of another auxiliary metal element causes the first metal element to dissolve faster in the fission material, which is why the speed of the above-mentioned thermal treatment, which was from 200-300 hours with a single addition element, is reduced by at least 50 hours when two additive elements are used.
Mengdene av det første tilsetnings-element er små og de er enda mindre for det annet tilsetningselements vedkom-mende. De overstiger som regel ikke 2 pst. av vekten i det første tilfelle, og 1 vekts-pst. i det annet tilfelle, beregnet fra den rene uranmetallvekten. The amounts of the first additive element are small and they are even smaller for the second additive element. As a rule, they do not exceed 2 percent of the weight in the first case, and 1 percent by weight in the second case, calculated from the pure uranium metal weight.
Den første metalltilsetning kan fortrinnsvis være aluminium, zirkon, krom, titan, vanadium osv. The first metal addition can preferably be aluminum, zirconium, chromium, titanium, vanadium, etc.
Den annen metalltilsetning kan f. eks. være zirkonium (f. eks. 0,1 vekts-pst.), molybden, (f. eks. 0,5—1 vekts-pst.) eller et annet metall i det periodiske systems klasse 5 og innføres fortrinnsvis i form av en legering med uran. The other metal addition can e.g. be zirconium (e.g. 0.1% by weight), molybdenum (e.g. 0.5-1% by weight) or another metal in class 5 of the periodic table and is preferably introduced in the form of a alloy with uranium.
I henhold til en utførelsesform av fremgangsmåten til fremstilling av uran-legeringer blir tilsetningselementene til-satt til rent metallisk uran i de oven-nevnte mengder i ett eller flere trinn. Deretter blir det hele smeltet ved et trykk av ca. IO-4—10—5 mm Hg, hvoretter det smeltede bad opphetes til ca. 1500° C i tilstrekkelig lang tid til at det oppnås fullstendig oppløsning og avgassing. Deretter støpes det hele til f. eks. staver eller barrer, under betingelser som omtrent utelukker ok-sy das jon. According to one embodiment of the method for producing uranium alloys, the additive elements are added to pure metallic uranium in the above-mentioned amounts in one or more steps. The whole thing is then melted at a pressure of approx. IO-4—10—5 mm Hg, after which the molten bath is heated to approx. 1500° C for a sufficiently long time for complete dissolution and degassing to be achieved. The whole is then molded into e.g. rods or bars, under conditions that almost exclude ok-sy da ion.
Den legering som fåes ved den foran beskrevne utførelsesmåte er en legering med to faser og store korn som er meget forbedret i forhold til det rene metall hva angår mekaniske egenskaper og termisk utmatning. Men på grunn av den grove fordeling av den annen fase bør man ved en passende varmebehandling fjerne de følsomheter som er nevnt foran, og som fremdeles finnes på visse steder av metallmassen. The alloy obtained by the method described above is an alloy with two phases and large grains which is much improved compared to the pure metal in terms of mechanical properties and thermal fatigue. However, due to the coarse distribution of the second phase, the sensitivities mentioned above, which are still present in certain places of the metal mass, should be removed by a suitable heat treatment.
I denne hensikt blir den således erholdte legering opphetet til en slik temperatur at man etter et tilstrekkelig tidsfor-løp og uten at materialet har deformert seg ikke lenger gjenfinner annet enn spor av den annen fase som bevirker den nevnte følsomhet. Denne behandling skjer under et trykk av størrelsesorden 10—3 mm Hg for å unngå oksydering og ved en temperatur som er over 1000° C og under den temperatur ved hvilken legeringen begynner å smelte. Deretter bråkjøler man i et koldt oljebad likeledes under vakuum. Denne oppløsnings- eller homogeniserings-behandling av den faste fase som fordob-ler styrken av den rå støpte masse gir massen krystallinsk struktur av overgangs-karakter som kan utvikles videre til en mere stabil struktur ved en fornyet behandling eller anløpning. For this purpose, the alloy thus obtained is heated to such a temperature that, after a sufficient period of time and without the material having deformed, nothing but traces of the second phase which causes the aforementioned sensitivity can be found. This treatment takes place under a pressure of the order of 10-3 mm Hg to avoid oxidation and at a temperature above 1000° C and below the temperature at which the alloy begins to melt. It is then quenched in a cold oil bath, also under vacuum. This dissolution or homogenization treatment of the solid phase, which doubles the strength of the raw cast mass, gives the mass a crystalline structure of a transitional nature that can be further developed into a more stable structure by renewed treatment or tempering.
Denne sistnevnte behandling består i at metallmassen opphetes til en temperatur som ligger ved grensen for stabilitets-området av urans ortorhombiske fase (dvs. ca. 660° C), og dette i tilstrekkelig lang tid til at det oppnås en krystallrearrangering i grunnmassen — uran, — og en meget fin-kornet og meget jevn utfelling av den annen fase. Ved denne nye behandling får legeringen en ennå større styrke og en bedre motstandsevne mot termisk utmatning enn «solubiliserte» legeringer har. This latter treatment consists in the metal mass being heated to a temperature that lies at the limit of the stability range of uranium's orthorhombic phase (i.e. approx. 660° C), and this for a sufficiently long time to achieve a crystal rearrangement in the base mass — uranium, — and a very fine-grained and very uniform precipitation of the second phase. With this new treatment, the alloy gains an even greater strength and a better resistance to thermal fatigue than "solubilized" alloys have.
Nedenfor forklares oppfinnelsen nær-mere ved hjelp av eksempler. Below, the invention is explained in more detail by means of examples.
I et første eksempel hadde en uran-stang som veiet ca. 50 kg et lukkbart rom som ble fylt med ca. 0,4 pst. aluminium-granalier av 99,9 pst. renhet beregnet på stangens masse og 0,15 pst. zirkonium i form av en uran-zirkoniumlegering som inneholdt 2,5 vekts-pst. zirkonium. In a first example, a uranium rod weighing approx. 50 kg a lockable room that was filled with approx. 0.4 percent aluminum granules of 99.9 percent purity calculated on the mass of the rod and 0.15 percent zirconium in the form of a uranium-zirconium alloy which contained 2.5 percent by weight. zirconium.
Den således fylte stang ble opphetet i vakuum f. eks. ved høyfrekvensinduksjon (ca. 4—800 kgperioder) i en digel som var slik beskyttet at angrepet fra smeltet uran var begrenset til et minimum. Opphetnin-gen skjedde slik at det den hele tid ble opprettholdt et trykk på mellom 10—4 og IO—5 imm Hg i apparatets rom. Etter at massen var smeltet ble temperaturen he-vet til og holdt på ca. 1500° C i 30—45 min., hvoretter den smeltede masse fremdeles under vakuum ble helt ned i en passende støpeform. Nedhellingen skjedde ved tyng-dekraftens hjelp idet man i det ønskede øyeblikk og ved hjelp av en utenfra på-virkbar stang trakk ut en propp av ildfast materiale som var anbragt i beholderens bunn. Etter avkjøling i vakuum for å unngå oksydasjon av legeringen tas massen ut av formen. The rod thus filled was heated in a vacuum, e.g. by high-frequency induction (approx. 4-800 kg periods) in a crucible that was so protected that the attack from molten uranium was limited to a minimum. The heating took place in such a way that a pressure of between 10-4 and 10-5 mmHg was maintained throughout the apparatus's compartment. After the mass had melted, the temperature was raised to and maintained at approx. 1500° C for 30-45 min., after which the molten mass, still under vacuum, was poured into a suitable mould. The pouring took place with the help of gravity, when at the desired moment and with the help of an externally actuable rod, a plug of refractory material which was placed in the bottom of the container was pulled out. After cooling in a vacuum to avoid oxidation of the alloy, the mass is removed from the mold.
På denne måte kan man få støpeblok-ker som deretter omdannes til stenger eller staver ved laminering, hamring, trekking eller på annen måte. Man kan også direkte fremstille barrer som har en diameter av 16—36 mm og en lengde av 30—50 cm. In this way, casting blocks can be obtained which are then converted into bars or rods by lamination, hammering, drawing or in other ways. Ingots with a diameter of 16-36 mm and a length of 30-50 cm can also be directly produced.
Den således erholdte legering blir deretter underkastet en første varmebehandling. Denne består i at legeringen under et trykk av ca. 10—3 mm Hg i ca. 50 timer opphetes til ca. 1050° C i en motstands-ovn som står i forbindelse med et oljebad. For at det skal unngås ikke-kontrollerbar utfelling under avkjølingen til omgivelse-nes temperatur, lar man etter at oppløs-ningsbehandlingen er ferdig legeringen falle ned i badet av kold olje, hvorved det oppnås en bråkjøling ved hvilken aluminiu-met holdes i overmettet oppløsning i uran-grunnmassen, og da befinner seg i en me-tastabil overgangstilstand. Denne legerings morfologiske tilstand blir deretter stabili-sert ved en ny varmebehandling, som består i at legeringen under vakuum opphetes The alloy thus obtained is then subjected to a first heat treatment. This consists in the alloy under a pressure of approx. 10—3 mm Hg for approx. 50 hours is heated to approx. 1050° C in a resistance furnace connected to an oil bath. In order to avoid uncontrollable precipitation during the cooling to the ambient temperature, after the solution treatment is finished the alloy is allowed to fall into the bath of cold oil, whereby a rapid cooling is achieved whereby the aluminum is kept in supersaturated solution in the uranium base mass, and is then in a metastable transition state. This alloy's morphological state is then stabilized by a new heat treatment, which consists in the alloy being heated under vacuum
til ca. 600° C i noen ti-minutter. Man får to approx. 600° C for a few ten minutes. You get
da et metall hvis Vickers-hårdhet er ca. then a metal whose Vickers hardness is approx.
420 til forskjell fra vanlig urans 210, og 420 as opposed to ordinary uranium's 210, and
som ikke lenger deformeres når det utset-tes for de forskjellige termiske utmat-ningspåkj enninger. which is no longer deformed when it is exposed to the various thermal stresses.
I et annet utførelseseksempel ble In another exemplary embodiment,
ca. 52 kg tetrafluoruran behandlet etter en about. 52 kg of tetrafluorouranium treated after a
av de vanlige reduksjonsmetoder med 19 of the usual reduction methods with 19
kg kalsium som på forhånd var blitt til-blandet ca. 150 g aluminiumspon eller 250 kg of calcium which had been mixed beforehand approx. 150 g aluminum shavings or 250
g aluminiumpulver. g aluminum powder.
Man får da rå støpestykker som for å You then get raw castings as if to
avgasses smeltes igjen under tilsetning av is degassed and melted again while adding
fortrinnsvis 0,15 vektsdeler zirkonium i preferably 0.15 parts by weight of zirconium i
form av en uran-zirkoniumlegering som form of a uranium-zirconium alloy which
inneholder 2y2 vekts-pst. zirkonium. Disse contains 2y2 wt. zirconium. These
stykker blir så underkastet de varmebe-handlinger som er beskrevet ovenfor. pieces are then subjected to the heat treatments described above.
Claims (2)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| US41001064A | 1964-11-09 | 1964-11-09 |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| NO121038B true NO121038B (en) | 1971-01-11 |
Family
ID=23622845
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO16040365A NO121038B (en) | 1964-11-09 | 1965-11-09 |
Country Status (10)
| Country | Link |
|---|---|
| BE (1) | BE671143A (en) |
| CH (2) | CH461453A (en) |
| DE (1) | DE1543029A1 (en) |
| DK (1) | DK116727B (en) |
| ES (1) | ES319383A1 (en) |
| GB (1) | GB1120256A (en) |
| IL (1) | IL24593A (en) |
| LU (1) | LU49691A1 (en) |
| NO (1) | NO121038B (en) |
| SE (1) | SE335117B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE19519008A1 (en) * | 1995-05-24 | 1996-11-28 | Hoechst Ag | New metal oxide catalysts containing ruthenium and selenium or sulfur, and a process for their preparation and their use |
| DE19519004A1 (en) * | 1995-05-24 | 1996-11-28 | Hoechst Ag | New metal oxide catalysts containing selenium and ruthenium as well as a process for their production and their use |
-
1965
- 1965-10-20 BE BE671143D patent/BE671143A/xx unknown
- 1965-10-22 LU LU49691D patent/LU49691A1/xx unknown
- 1965-11-03 GB GB4660965A patent/GB1120256A/en not_active Expired
- 1965-11-08 IL IL2459365A patent/IL24593A/en unknown
- 1965-11-08 DK DK573265A patent/DK116727B/en unknown
- 1965-11-09 ES ES0319383A patent/ES319383A1/en not_active Expired
- 1965-11-09 CH CH1498967A patent/CH461453A/en unknown
- 1965-11-09 SE SE1443665A patent/SE335117B/xx unknown
- 1965-11-09 NO NO16040365A patent/NO121038B/no unknown
- 1965-11-09 CH CH1542965A patent/CH450384A/en unknown
- 1965-11-09 DE DE19651543029 patent/DE1543029A1/en active Pending
Also Published As
| Publication number | Publication date |
|---|---|
| CH450384A (en) | 1968-01-31 |
| GB1120256A (en) | 1968-07-17 |
| DK116727B (en) | 1970-02-09 |
| IL24593A (en) | 1969-07-30 |
| DE1543029A1 (en) | 1969-09-11 |
| ES319383A1 (en) | 1966-05-01 |
| LU49691A1 (en) | 1967-04-24 |
| SE335117B (en) | 1971-05-17 |
| CH461453A (en) | 1968-08-31 |
| BE671143A (en) | 1966-04-20 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN101440436B (en) | Purified smelting technique for high-temperature superalloy | |
| US2548897A (en) | Process for melting hafnium, zirconium, and titanium metals | |
| EP4023779A1 (en) | Smelting process for high-niobium high-temperature alloy large-size cast ingot, and high-niobium high-temperature alloy large-size cast ingot | |
| CN113564391A (en) | Method for eliminating primary silicon in hypereutectic aluminum-silicon alloy by utilizing melt circulation overheating | |
| JP2024527224A (en) | Alloy structural steel and its manufacturing method | |
| JP2024526979A (en) | High strength composite modified aluminum alloy part and manufacturing method thereof | |
| CN106834766B (en) | A method of preparing large scale high alloy constituent content magnesium alloy ingot | |
| NO121038B (en) | ||
| CN102965556A (en) | Multi-element Mg-Zn-Al based magnesium alloy and preparation method thereof | |
| NO123761B (en) | ||
| CN104988371B (en) | Magnesium-rare earth suitable for sand casting and preparation method thereof | |
| US4049470A (en) | Refining nickel base superalloys | |
| US3177069A (en) | Methods of manufacturing fissionable materials for use in nuclear reactors | |
| US2976192A (en) | Process for improving the quality of copper-zirconium alloy castings | |
| CN1107740C (en) | Al and Mg alloy solid solution or homogenizing heat treatment method | |
| US3508914A (en) | Methods of forming and purifying nickel-titanium containing alloys | |
| CN111531135A (en) | Production process of aluminum-silicon intermediate alloy | |
| SE203545C1 (en) | ||
| RU2362651C1 (en) | Method for production of ingots and cast articles out of intermetallic alloys | |
| Yang et al. | Microstructure Evolution in the Mushy Zone of a β‐Solidifying TiAl Alloy under Different Cooling Processes | |
| JPH04272147A (en) | Production of titanium | |
| US2875034A (en) | Production of metals | |
| CN104152771A (en) | Silver and rare earth-containing high-strength heat-resistant magnesium alloy and preparation method thereof | |
| SU367167A1 (en) | ||
| CN104131201A (en) | Mg-Al based alloy refining modificator as well as preparation method and applications thereof |