NO141942B - PROCEDURE FOR TREATMENT OF ALUMINUM ALLOYS - Google Patents
PROCEDURE FOR TREATMENT OF ALUMINUM ALLOYS Download PDFInfo
- Publication number
- NO141942B NO141942B NO751114A NO751114A NO141942B NO 141942 B NO141942 B NO 141942B NO 751114 A NO751114 A NO 751114A NO 751114 A NO751114 A NO 751114A NO 141942 B NO141942 B NO 141942B
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- Prior art keywords
- temperature
- alloy
- liquid phase
- solid
- solidus
- Prior art date
Links
- 238000000034 method Methods 0.000 title claims description 11
- 229910000838 Al alloy Inorganic materials 0.000 title claims description 5
- 239000007791 liquid phase Substances 0.000 claims description 24
- 229910045601 alloy Inorganic materials 0.000 claims description 21
- 239000000956 alloy Substances 0.000 claims description 21
- 239000007787 solid Substances 0.000 claims description 12
- 210000001787 dendrite Anatomy 0.000 claims description 6
- 239000007788 liquid Substances 0.000 claims description 6
- 239000007790 solid phase Substances 0.000 claims description 6
- 239000012071 phase Substances 0.000 claims description 5
- 238000003756 stirring Methods 0.000 claims description 5
- 238000010438 heat treatment Methods 0.000 claims description 3
- 229910018125 Al-Si Inorganic materials 0.000 claims description 2
- 229910018182 Al—Cu Inorganic materials 0.000 claims description 2
- 229910018520 Al—Si Inorganic materials 0.000 claims description 2
- 230000007704 transition Effects 0.000 claims description 2
- 238000001816 cooling Methods 0.000 description 7
- 239000000203 mixture Substances 0.000 description 5
- 238000003303 reheating Methods 0.000 description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 4
- 229910052749 magnesium Inorganic materials 0.000 description 3
- 239000011777 magnesium Substances 0.000 description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 2
- 229910000861 Mg alloy Inorganic materials 0.000 description 2
- NBIIXXVUZAFLBC-UHFFFAOYSA-N Phosphoric acid Chemical compound OP(O)(O)=O NBIIXXVUZAFLBC-UHFFFAOYSA-N 0.000 description 2
- WGLPBDUCMAPZCE-UHFFFAOYSA-N Trioxochromium Chemical compound O=[Cr](=O)=O WGLPBDUCMAPZCE-UHFFFAOYSA-N 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 2
- -1 aluminum-zinc-magnesium Chemical compound 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 239000010949 copper Substances 0.000 description 2
- 238000002474 experimental method Methods 0.000 description 2
- 238000005242 forging Methods 0.000 description 2
- 229910052748 manganese Inorganic materials 0.000 description 2
- 239000011572 manganese Substances 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 238000003825 pressing Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 230000003313 weakening effect Effects 0.000 description 2
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 238000003475 lamination Methods 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 229910001092 metal group alloy Inorganic materials 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 235000011007 phosphoric acid Nutrition 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 238000004080 punching Methods 0.000 description 1
- 230000035939 shock Effects 0.000 description 1
- 239000010703 silicon Substances 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 230000002459 sustained effect Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 239000011701 zinc Substances 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
- B22D21/002—Castings of light metals
- B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/004—Thixotropic process, i.e. forging at semi-solid state
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/12—Making non-ferrous alloys by processing in a semi-solid state, e.g. holding the alloy in the solid-liquid phase
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Forging (AREA)
- Heat Treatment Of Nonferrous Metals Or Alloys (AREA)
- Continuous Casting (AREA)
- Extrusion Of Metal (AREA)
- Manufacture And Refinement Of Metals (AREA)
- Metal Extraction Processes (AREA)
- Manufacture Of Alloys Or Alloy Compounds (AREA)
- ing And Chemical Polishing (AREA)
- Chemical Treatment Of Metals (AREA)
Description
Foreliggende oppfinnelse angår en fremgangsmåte for behandling The present invention relates to a method for treatment
av aluminium-legeringer som lar seg varmebehandle, av typen Al-Si og Al-Cu-legeringer for å bringe dem til en blandingstilstand av fast og flytende fase under opprettholdelse av fast form, hvor legeringen bringes opp på en temperatur mellom solidus- og likvidus-temperaturene og holdes der i en tid på of heat-treatable aluminum alloys of the Al-Si and Al-Cu alloys to bring them to a mixed state of solid and liquid phase while maintaining solid form, where the alloy is brought up to a temperature between solidus and liquidus -temperatures and kept there for a time of
mellom noen minutter og noen timer, og det særegne består i at varmebehandlingen forsettes uten omrøring inntil en vektmengde av legeringen på under 40% og fortrinnsvis under 35% er brakt til flytende tilstand, slik at den faste dendrittfase har be- between a few minutes and a few hours, and the peculiarity is that the heat treatment continues without stirring until a weight amount of the alloy of less than 40% and preferably less than 35% has been brought to a liquid state, so that the solid dendritic phase has
gynt å gå over i kuleform. tend to go into a ball shape.
Fra det franske patent nr. 2141979 er det kjent en legering An alloy is known from French patent no. 2141979
som hva relative mengder av fast og flytende fase angår, meget nær svarer til det samme forhold som fremkommer ved gjennom-føringen av foreliggende fremgangsmåte. I patentet utgjør imidlertid en kraftig omrøring et vesentlig trekk ved fremstillingen, mens foreliggende fremgangsmåte som angitt gjennomføres uten omrøring. Foreliggende fremgangsmåte er således vesentlig enklere og dermed billigere, og lar seg meget lett gjennomføre which, as far as the relative amounts of solid and liquid phase are concerned, very closely corresponds to the same ratio that appears when carrying out the present method. In the patent, however, vigorous stirring is an essential feature of the preparation, while the present method, as indicated, is carried out without stirring. The present method is thus significantly simpler and therefore cheaper, and can be implemented very easily
i industriell målestokk. on an industrial scale.
Det er vel kjent av hvis en metall-legering i fast tilstand oppvarmes gradvis, vil de første spor av flytende fase vise seg i det øyeblikk solidus-temperaturen nås, og at forholdet mellom fast fase og flytende fase utvikler seg inntil full- It is well known that if a metal alloy in the solid state is heated gradually, the first traces of liquid phase will appear at the moment the solidus temperature is reached, and that the relationship between solid phase and liquid phase develops until full-
stendig smeltning i det øyeblikk likvidus-temperaturen nås. permanent melting the moment the liquidus temperature is reached.
Det har nå helt overraskende vist seg at hvis en fast metall- It has now been shown, quite surprisingly, that if a solid metal
legering bringes opp på en temperatur mellom solidus-tempera- alloy is brought up to a temperature between the solidus tempera-
turen og likvidus-temperaturen, vil det forgrenede dendritt-nettverk i primærfasen, som dog holder seg stort sett fast. under behandlingen, undergå en struktur-degradering og utvikle seg gradvis til en kuleform hvis dimensjoner avhenger av fin- the trip and the liquidus temperature, the branched dendrite network in the primary phase will, however, remain largely fixed. during the treatment, undergo a structural degradation and gradually develop into a spherical shape whose dimensions depend on the fine-
heten av den opprinnelige dendritt-struktur, men i alminnelig- heat of the original dendrite structure, but in general
het ligger mellom 100 og 400 mikrometer. it lies between 100 and 400 micrometres.
Det har videre vist seg at en legering som holdes på en tempera- It has also been shown that an alloy held at a tempera-
tur mellom solidus- og likvidus-temperaturene, beholder ut- trip between the solidus and liquidus temperatures, retains out-
seendet av et fast legeme hvis den relative mengde flytende fase ikke overstiger 60%. Et slikt produkt må imidlertid håndteres med forsiktighet og et støt eller en stor påkjenning medfører ofte en hel eller delvis svekning.Så snart den relative mengde av flytende fase synker til omtrent 50%.og fortrinnsvis under 35%, kan håndteringen foregå med minimal forsiktighet. seen as a solid body if the relative amount of liquid phase does not exceed 60%. However, such a product must be handled with care and a shock or a great stress often results in a complete or partial weakening. As soon as the relative amount of liquid phase drops to about 50% and preferably below 35%, handling can take place with minimal care.
Ved en mengde av ca. 20% flytende fase kan produktet håndteres omtrent som et vanlig fast stoff. At a quantity of approx. 20% liquid phase, the product can be handled much like a normal solid substance.
Det har nå vist seg at en legering som holdes mellom solidus- It has now been shown that an alloy held between the solidus
og likvidus-temperaturene, og på en slik temperatur at den forholdsvise mengde flytende fase er mindre enn 40%, er særlig godt egnet til å tilformes ved hjelp av alle de fremgangsmåter som vanlig anvendes i forbindelse med legeringer i fast til- and the liquidus temperatures, and at such a temperature that the relative amount of liquid phase is less than 40%, is particularly well suited to forming using all the methods that are normally used in connection with alloys in solid form
stand, f.eks. trekking, ekstrudering, laminering, pressing, stansing, smiing osv. condition, e.g. drawing, extrusion, lamination, pressing, punching, forging, etc.
Overgangen fra den faste fase med dendritt-struktur til en kulestruktur, gir den legering som er behandlet i henhold til oppfinnelsen en betydelig forbedret evne til plastisk flyting i fast tilstand, slik at det er mulig både å øke flytehastig- The transition from the solid phase with a dendrite structure to a spherical structure gives the alloy treated according to the invention a significantly improved ability to plastic flow in the solid state, so that it is possible to both increase the flow rate
heten og nedsett den kraft som kreves av maskinen. Disse nye egenskaper svarer til en særlig tilstand av legeringen, som kalles "rheotrop". the heat and reduce the power required by the machine. These new properties correspond to a special state of the alloy, which is called "rheotropic".
Det skal understrekes at rheotropien ikke er en enkel følge av temperaturhevningen. I betraktning av de vanskeligheter som er forbundet med fremgangsmåter for omdannelse av visse legeringer i fast tilstand, ville det ligge nær å anta at det var tilstrekkelig å øke temperaturen ved f.eks. trekkingen, for der--ved å nedsette den kraft som kreves av pressen. Erfaring viser imidlertid at temperaturen 4 50 °C som er valig ved trekking av aluminiumlegeringer, f.eks. AU4 SG (som inneholder ca. 4% It must be emphasized that the rheotropy is not a simple consequence of the temperature rise. In view of the difficulties associated with methods for the transformation of certain alloys in the solid state, it would be close to assume that it was sufficient to increase the temperature by e.g. the draw, because there--by reducing the force required by the press. Experience shows, however, that the temperature 4 50 °C which is optional when drawing aluminum alloys, e.g. AU4 SG (containing approx. 4%
Cu, 1% Si, 0,8% Mn og 0,5% Mg) er maksimal og aldri tidligere er overskredet i industriell praksis. Over denne temperatur legges det merke til at metallets plastisitet, som passerer et maksimum mellom 420 og 450 °C vil synke igjen og, dessuten vil den dynamiske kraft som utvikles ved trekkstenen føre med seg en slik temperaturstigning at profilet blir gjort delvis flytende, altså ubrukelig. Trekking i rheotrop tilstand vil derimot frembringe forholdsvis liten dynamisk kraft ved trekkstenen, Cu, 1% Si, 0.8% Mn and 0.5% Mg) is maximum and has never before been exceeded in industrial practice. Above this temperature, it is noticed that the metal's plasticity, which passes a maximum between 420 and 450 °C, will decrease again and, furthermore, the dynamic force developed at the drawstone will bring with it such a temperature rise that the profile is made partially liquid, i.e. unusable . Drawing in a rheotropic state, on the other hand, will produce relatively little dynamic force at the drawing stone,
og det er tilstrekkelig med en forholdsvis svak kjølestrøm for, i det ekstruderte profil, å størkne de små mengder flytende fase som er jevnt fordelt og som ikke påvirker kohesjonen. Dessuten blir slitasjen i verktøyet sterkt nedsatt. and a relatively weak cooling current is sufficient to solidify, in the extruded profile, the small amounts of liquid phase which are evenly distributed and which do not affect the cohesion. In addition, wear and tear on the tool is greatly reduced.
For å illustrere virkningen av fremgangsmåten i henhold til oppfinnelsen, skal det ved hjelp av mikrofotografier foretas en sammenlikning mellom strukturene i aluminiumlegeringen AU4 GS behandlet på forskjellige måter. Fig. 1 som er et mikrofotografi med forstørrelse 50, viser strukturen i en legering AU4 GS fremstillet på vanlig måte ved halvkontinuerlig støping av en barre. Dendritt-strukturen er klart synlig. Fig. 2 er et mikrofotografi med forstørrelse 50, av samme legering, behandlet i henhold til oppfinnelsen. Den var holdt i 1 time på 6 20 °C, hvilket svarer til en forholdsvis vektmengde flytende fase på ca. 25%. To illustrate the effect of the method according to the invention, a comparison shall be made by means of microphotographs between the structures in the aluminum alloy AU4 GS treated in different ways. Fig. 1, which is a photomicrograph with magnification 50, shows the structure of an alloy AU4 GS produced in the usual way by semi-continuous casting of an ingot. The dendrite structure is clearly visible. Fig. 2 is a photomicrograph with magnification 50, of the same alloy, treated according to the invention. It had been kept for 1 hour at 6 20 °C, which corresponds to a relative weight amount of liquid phase of approx. 25%.
Mikrofotografiene ble tatt etter et anodisk angrep i en blanding som inneholdt 1000 cm 3 ortofosforsyre og 30 g kromsyreanhydrid ved 90 °C i 1-2 min., under en slik likespenning at strømtett-heten på o prøvestykket var ca. 0,2 A/dm 2. De sorte flekker i fig. 2 er kuler av primærfasen som skyldes dendritt-svekningen. Det vil ofte legges merke til at det inne i kulene forekommer sfæriske rosetter med hvit omkrets som skyldes små flytende dråper som er blitt innesluttet under varmebehandlingen. The photomicrographs were taken after an anodic attack in a mixture containing 1000 cm 3 of orthophosphoric acid and 30 g of chromic anhydride at 90 °C for 1-2 min., under such a direct voltage that the current density on the o sample was approx. 0.2 A/dm 2. The black spots in fig. 2 are spheres of the primary phase due to dendrite weakening. It will often be noticed that inside the balls there are spherical rosettes with a white circumference, which are due to small liquid droplets that have been trapped during the heat treatment.
Hvor lenge temperaturen skal holdes for å bevirke at kule-strukturen viser seg, og for å oppnå plastisk flytning i fast tilstand, avhenger av legeringstypen og, for en gitt legering, med høyden av den varige temperatur, som dessuten bestemmer forholdet mellom flytende og fast fase. Eksempelvis kan den være fra noen minutter til fire timer, og fortrinnsvis fra ca. 5 til 60 minutter for aluminium-sink-magnesium-legeringer eller aluminium-silisium-kobber-magnesium-legeringer. How long the temperature must be maintained to cause the spheroid structure to appear, and to achieve plastic flow in the solid state, depends on the type of alloy and, for a given alloy, on the height of the sustained temperature, which also determines the ratio of liquid to solid phase. For example, it can be from a few minutes to four hours, and preferably from approx. 5 to 60 minutes for aluminum-zinc-magnesium alloys or aluminum-silicon-copper-magnesium alloys.
Sylinderformede barrer, fremstillet ved kontinuerlig eller halv-kontinuerlig kokillestøping og behandlet i henhold til oppfinnelsen kan behandles i f.eks. en stang-presse. Etter å være ført inn i beholderen for maskinen, kan de ekstruderes i profil-form forutsatt at det forligger muligheter for passende kjøling av trekk-dysen og av det profil som kommer ut av denne, f.eks. kjøling ved hjelp av vann eller luft. Denne kjøling bør være tilstrekkelig til å fryse størstedelen av den flytende fraksjon som inneholdes i den trukkede barre. Cylindrical ingots, produced by continuous or semi-continuous mold casting and treated according to the invention can be treated in e.g. a bar press. After being fed into the container for the machine, they can be extruded in profile form provided that there are opportunities for suitable cooling of the drawing die and of the profile coming out of it, e.g. cooling using water or air. This cooling should be sufficient to freeze the majority of the liquid fraction contained in the drawn ingot.
Denne fremgangsmåte har følgende fordeler: This procedure has the following advantages:
- forholdet mellom trekkingen og/eller trekk-hastigheten er høyere, - trekk-trykket er betydelig nedsatt, med derav følgende nedsatt slitasje på verktøyet. - the ratio between the pull and/or the pull speed is higher, - the pull pressure is significantly reduced, with consequent reduced wear on the tool.
Det har også vist seg at hvis kjølingen foretas.ned til værelsestemperatur eller til en eller annen temperatur som ligger under solidustemperaturen for en behandlet barre og det deretter foretas gjennoppvarming til en temperatur mellom It has also been shown that if the cooling is carried out down to room temperature or to some temperature below the solidus temperature of a treated ingot and reheating is then carried out to a temperature between
solidus og likvidus som tilsvarer høyst 40% flytende fase, solidus and liquidus which correspond to a maximum of 40% liquid phase,
vil denne barre så å si straks gjenfinne sine rheotrope egenskaper, noe som beviser at det faktisk har foregått en varig endring i strukturen og det er fremkommet en ny struktur. this bar will, so to speak, immediately regain its rheotropic properties, which proves that a permanent change in structure has actually taken place and a new structure has emerged.
Denne gjenoppvarming kan foretas ved en temperatur som er høyere, This reheating can be carried out at a temperature that is higher,
lik eller lavere enn temperaturen for den første behandling alt etter den forholdvise mengde flytende fase som ønskes. equal to or lower than the temperature for the first treatment depending on the relative amount of liquid phase desired.
Det skal nå beskrives noen eksempler på hvorledes fremgangs- Some examples will now be described of how progress
måten i henhold til oppfinnelsen kan gjennomføres. Alle trekk-prøvene i eksemplene 1-7 ble foretatt i en Loewy-presse på the way according to the invention can be carried out. All the tensile tests in examples 1-7 were carried out in a Loewy press on
800 tonn. 800 tonnes.
Eksempel 1 Example 1
Tre sylinderformede barrer med en diameter på 100 mm og en Three cylindrical bars with a diameter of 100 mm and a
lengde på 300 mm av nystøpt legering AU4 SG, som består av aluminium med 0,42% jern, 0,91% silisium, 4,24% kobber, 0,82% length of 300 mm of newly cast alloy AU4 SG, which consists of aluminum with 0.42% iron, 0.91% silicon, 4.24% copper, 0.82%
mangan og 0,51% magnesium, ble holdt i 15 min. ved temperaturen. manganese and 0.51% magnesium, was held for 15 min. at the temperature.
barre A - 585 °C bar A - 585 °C
barre B - 59 5 °C barre B - 59 5 °C
barre C - 605 °C barre C - 605 °C
noe som tilsvarte henholdsvis which corresponded respectively
ca. 6% flytende fase i barre A about. 6% liquid phase in ingot A
ca. 8% flytende fase i barre B about. 8% liquid phase in bar B
ca. 13% flytende fase i barre C. about. 13% liquid phase in bar C.
I tre forsøk som fulgte etter hverandre ble de ført inn i beholderen som på forhånd var oppvarmet til 420-450 °C i 800 tonn-pressen og straks trukket med en hastighet på 8 m/min. i form av et profil med rektangulært tverrsnitt 40 x 3 mm. Vann-kjølingen av trekk-dysen ble innstillet slik at temperaturen i profilet ved utgangen fra dysen var ca. 450 °C. Håndteringen av barrene foregikk under vanlige forhold og trekkingen ble utført på tilfredssti llende måte. For hver barre bl e det oppnådd ca. 15 m profil med upåklagelig overflateutseende. De mekaniske egenskaper for profilene ble målt på prøvestykker: In three successive trials, they were introduced into the container which had previously been heated to 420-450 °C in the 800 tonne press and immediately drawn at a speed of 8 m/min. in the form of a profile with a rectangular cross-section 40 x 3 mm. The water cooling of the draft nozzle was set so that the temperature in the profile at the exit from the nozzle was approx. 450 °C. The handling of the bars took place under normal conditions and the drawing was carried out in a satisfactory manner. For each bar, approx. 15 m profile with impeccable surface appearance. The mechanical properties of the profiles were measured on test pieces:
1) Rå-trekk 1) Raw move
2) Etter 8 timer ved 175 °C 2) After 8 hours at 175 °C
3) Herdet i vann etter å være holdt i 2 timer ved 505 °C deretter 8 timer ved 175 °C (tilstand T6) , med følgende resultater: 3) Cured in water after being held for 2 hours at 505 °C then 8 hours at 175 °C (condition T6), with the following results:
Disse egenskaper, som var omtrent uavhengige av behandlings-temperaturen, var helt tilfredsstillende og likner dem som oppnås ved produkter som er trukket på vanlig måte. These properties, which were approximately independent of the treatment temperature, were completely satisfactory and similar to those obtained with products drawn in the usual way.
Eksempel 2 Example 2
En barre av AU'4 'SG med diameter 100 mm og samme sammensetning som i eksempel 1, ble behandlet i henhold til oppfinnelsen, i 15 min. ved 572 °C slik at det fremkom ca. 4% flytende fase. Barren ble trukket slik at det ble oppnådd en rund stang med A bar of AU'4'SG with a diameter of 100 mm and the same composition as in example 1 was treated according to the invention for 15 min. at 572 °C so that approx. 4% liquid phase. The bar was drawn so that a round bar was obtained with
en diameter på 20 mm, dvs. et trekkforhold på 25, med en hastighet på 3 m/min. Det midlere trykk på legemet i pressen a diameter of 20 mm, i.e. a draft ratio of 25, at a speed of 3 m/min. The average pressure on the body in the press
2 2
var fastlagt på 15 N/mm . was set at 15 N/mm.
Samme forsøk, utført på vanlig måte ved varm-trekning på en barre som ikke var behandlet i henhold til oppfinnelsen, krevet et trykk på 2 2 N/mm 2,■altså ca. 50% høyere trykk. The same test, carried out in the usual way by hot-drawing on a bar that had not been treated according to the invention, required a pressure of 2 2 N/mm 2 , i.e. approx. 50% higher pressure.
De trukkede stenger hadde følgende egenskaper: The drawn bars had the following properties:
For den stang som var trukket i henhold til oppfinnelsen, vil det ses at en enkel behandling i 8 timer ved 175 °C gjør det mulig For the bar drawn according to the invention, it will be seen that a simple treatment for 8 hours at 175 °C makes it possible
å oppnå mekaniske egenskaper som er bedre enn de som fore-ligger i tilsvarende tilstand etter vanlig trekning. to achieve mechanical properties that are better than those present in a similar state after normal drawing.
Eksempel 3 Example 3
Av to små barrer av AZ5G som består av aluminium, 4,40% sink, 1,18% magnesium, med diameter 100 mm, ble en trukket på vanlig måte, den annen etter behandling i henhold til oppfinnelsen, nemlig til 30 mm ved 620 °C slik at det fremkom 4% flytende fase. Of two small ingots of AZ5G consisting of aluminum, 4.40% zinc, 1.18% magnesium, with a diameter of 100 mm, one was drawn in the usual way, the other after treatment according to the invention, namely to 30 mm at 620 °C so that 4% liquid phase appeared.
Det ble trukket en rund stang med en diameter på 20 mm med en hastighet på 13,2 m/min. A round rod with a diameter of 20 mm was drawn at a speed of 13.2 m/min.
Det trykk som var nødvendit var 15,5 N/mm 2 for den barre som ikke var behandlet og 11,8 N/mm 2 for den barre som var behandlet i henhold til oppfinnelsen, altså en nedsettelse av presse-kraften på 24%. The pressure that was necessary was 15.5 N/mm 2 for the ingot that had not been treated and 11.8 N/mm 2 for the ingot that had been treated according to the invention, i.e. a reduction in the pressing force of 24%.
Eksempel 4 Example 4
To barrer av AZ5G, med samme sammensetning som i eksempel 3 Two ingots of AZ5G, with the same composition as in example 3
ble trukket med en bro-dyse, for å fremstille et hulprofil med kvadratisk tverrsnitt 25 x 25 mm og tykkelse 2 mm. Den ene var ikke behandlet, den annen behandlet i henhold til oppfinnelsen i 20 min. ved 6 25 °C slik at det ble dannet 7% flytende fase. was drawn with a bridge die to produce a hollow profile with a square cross-section of 25 x 25 mm and a thickness of 2 mm. One was not treated, the other treated according to the invention for 20 min. at 6 25 °C so that 7% liquid phase was formed.
Det trykk som var nødvendig var 28 N/mm 2 for den barre som The pressure required was 28 N/mm 2 for the bar which
ikke var behandlet og 23,8 N/mm 2 for den som var behandlet, altså en nedsettelse på 17%. had not been treated and 23.8 N/mm 2 for the one that had been treated, i.e. a reduction of 17%.
Eksempel 5 Example 5
To barrer av AU4 SG med samme sammensetning og samme dimensjon som i eksempel 1, ble trukket i en bro-dyse, den ene ikke behandlet, den annen behandlet i henhold til oppfinnelsen i 30 min. ved 585 °C, slik at det ble dannet 6% flytende fase, for å oppnå et hulprofil med kvadratisk tverrsnitt 25 x 25 mm og en tykkelse på 2 mm. Two ingots of AU4 SG with the same composition and the same dimensions as in example 1 were drawn in a bridge die, one untreated, the other treated according to the invention for 30 min. at 585 °C, so that 6% liquid phase was formed, to obtain a hollow profile with a square cross-section of 25 x 25 mm and a thickness of 2 mm.
Trekkingen av AU4 SG i en bro-dy se ble ikke foretatt på vanlig måte. Den ville, i dette spesielle tilfelle ha ført til - dårlige resultater, et dårlig overflate-utseende og kreve et trykk på 29 N/mm 2, nær den grense som gjelder for 800 tonn-pressen. The draw of the AU4 SG in a bro-dy see was not done in the usual way. It would, in this particular case, have led to - poor results, a poor surface appearance and required a pressure of 29 N/mm 2 , close to the limit applicable to the 800 ton press.
Derimot gav trekkingen av den barre som var behandlet i henhold til oppfinnelsen utmerkede resultater og krevet bare et trykk på 21 "N/mm . In contrast, the drawing of the ingot treated according to the invention gave excellent results and only required a pressure of 21 N/mm.
Eksempel 6 Example 6
En barre av AU4 SG, med samme sammensetning og samme dimensjon som i eksempel 1 ble behandlet, i henhold til oppfinnelsen ved å holdes i 15 min. ved 620 °C, slik at det ble 25% flytende fase. Deretter ble den ført inn i beholderen for trekk-pressen. For å unngå enhver fase for deformering, ble behandlingen A bar of AU4 SG, with the same composition and the same dimensions as in example 1 was treated, according to the invention by holding for 15 min. at 620 °C, so that there was 25% liquid phase. It was then fed into the container for the draw press. To avoid any phase of deformation, the treatment was
og overføringen av barren fra gejnoppvarmningsovnen til pressen utført i en halvsirkelformet vannrett vugge. and the transfer of the ingot from the reheating furnace to the press carried out in a semi-circular horizontal cradle.
Det ble ekstrudert et profil på 40 x 3 mm uten noen vanskelig-het, med et trykk som ikke oversteg 22 N/mm 2. Den 800 tonn-presse som ble brukt i dette forsøk, gjorde det ikke mulig å trekke en 100 mm barre forvarmet til 420/450 °C av AU4 SG til 40 x 3 mm under vanlige forhold. A 40 x 3 mm profile was extruded without any difficulty, with a pressure not exceeding 22 N/mm 2 . The 800 ton press used in this experiment did not make it possible to draw a 100 mm bar preheated to 420/450 °C of AU4 SG to 40 x 3 mm under normal conditions.
Ved å gjøre bruk av oppfinnelsen ble det således i dette tilfelle oppnådd en meget stor fordel. By making use of the invention, a very large advantage was thus achieved in this case.
Eksempel 7 Example 7
En sylinderformet barre med diameter på 100 mm og lengde 300 mm av legering AU4 SG ble holdt i 15 min. ved 585 °C for å danne ca. 6% flytende fase, derpå kjølet til væreIsestemperatur, der på gjenoppvarmet til 595 °C og uten opphold ført inn i beholderen som var forvarmet til 420-450 °C i en 800 tonn trekk-presse, og straks trukket med en hastighet på 8 m/min. til et profil med rektangulært tverrsnitt 40 x 3 mm. Vannkjølingen av dysen var innstillet slik at profil-temperaturen ved utgangen fra dysen var ca. 450 °C. A cylindrical ingot of diameter 100 mm and length 300 mm of alloy AU4 SG was held for 15 min. at 585 °C to form approx. 6% liquid phase, then cooled to room temperature, then reheated to 595 °C and without delay fed into the container which had been preheated to 420-450 °C in an 800 ton drawing press, and immediately drawn at a speed of 8 m /my. to a profile with a rectangular cross-section 40 x 3 mm. The water cooling of the nozzle was set so that the profile temperature at the outlet of the nozzle was approx. 450 °C.
Resultatene av dette forsøk var de samme som i eksempel IB, noe som viser at en enkel gjenoppvarming til den valgte temperatur, av en barre som på forhånd er behandlet i henhold til oppfinnelsen og deretter kjølet, øyeblikkelig gjenoppretter dens rheotrope egenskaper. The results of this experiment were the same as in Example IB, showing that a simple reheating to the selected temperature, of a bar previously treated according to the invention and then cooled, instantly restores its rheotropic properties.
Eksempel 8 Example 8
Ved senke-smiing ble det fremstillet en kompressor-drivstang A compressor drive rod was produced by drop forging
av AU4 SG med en avstand på 100 mm mellom aksene for stemplet og snekken. Vanligvis krever fremstillingen av en slik stang et tilformningstrinn og et slutt-trinn. of AU4 SG with a distance of 100 mm between the axes of the piston and the screw. Usually, the production of such a rod requires a forming step and a finishing step.
Ved å gjenoppvarme emnet i 15 min. ved 595 °C slik at det ble By reheating the subject for 15 min. at 595 °C so that it became
8% flytende fase, kunne denne stang oppnås i et eneste trinn, 8% liquid phase, this rod could be obtained in a single step,
med et trykk på 4 N/mm 2 i det hydrauliske kretsløp for pressen,.. i stedet for 10 N/mm 2 under vanlige forhold. with a pressure of 4 N/mm 2 in the hydraulic circuit of the press,.. instead of 10 N/mm 2 under normal conditions.
Claims (2)
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| LU69788A LU69788A1 (en) | 1974-04-04 | 1974-04-04 |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| NO751114L NO751114L (en) | 1975-10-07 |
| NO141942B true NO141942B (en) | 1980-02-25 |
| NO141942C NO141942C (en) | 1980-06-04 |
Family
ID=19727630
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO75751115A NO141943C (en) | 1974-04-04 | 1975-04-02 | PROCEDURE FOR TREATMENT OF ALUMINUM CASTLE ALLOYS |
| NO751114A NO141942C (en) | 1974-04-04 | 1975-04-02 | PROCEDURE FOR TREATMENT OF ALUMINUM ALLOYS |
Family Applications Before (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| NO75751115A NO141943C (en) | 1974-04-04 | 1975-04-02 | PROCEDURE FOR TREATMENT OF ALUMINUM CASTLE ALLOYS |
Country Status (17)
| Country | Link |
|---|---|
| JP (2) | JPS5615455B2 (en) |
| BE (2) | BE827496A (en) |
| CA (2) | CA1045783A (en) |
| CH (2) | CH603805A5 (en) |
| DD (2) | DD117372A5 (en) |
| DE (2) | DE2514355C3 (en) |
| ES (2) | ES436217A1 (en) |
| FR (2) | FR2266749B1 (en) |
| GB (2) | GB1502114A (en) |
| IL (2) | IL47001A (en) |
| IT (2) | IT1034783B (en) |
| LU (1) | LU69788A1 (en) |
| NL (2) | NL182415C (en) |
| NO (2) | NO141943C (en) |
| SE (2) | SE7503775L (en) |
| SU (1) | SU722494A3 (en) |
| ZA (2) | ZA752150B (en) |
Families Citing this family (29)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0004174B1 (en) * | 1978-03-08 | 1983-04-27 | Massachusetts Institute Of Technology | A process for refining a non-eutectic metal alloy |
| US4694882A (en) * | 1981-12-01 | 1987-09-22 | The Dow Chemical Company | Method for making thixotropic materials |
| US4694881A (en) * | 1981-12-01 | 1987-09-22 | The Dow Chemical Company | Method for making thixotropic materials |
| US4524820A (en) * | 1982-03-30 | 1985-06-25 | International Telephone And Telegraph Corporation | Apparatus for providing improved slurry cast structures by hot working |
| US4415374A (en) * | 1982-03-30 | 1983-11-15 | International Telephone And Telegraph Corporation | Fine grained metal composition |
| US4569218A (en) * | 1983-07-12 | 1986-02-11 | Alumax, Inc. | Apparatus and process for producing shaped metal parts |
| EP0139168A1 (en) * | 1983-09-20 | 1985-05-02 | Alumax Inc. | Fine grained metal composition |
| US5133811A (en) * | 1986-05-12 | 1992-07-28 | University Of Sheffield | Thixotropic materials |
| US4938052A (en) * | 1986-07-08 | 1990-07-03 | Alumax, Inc. | Can containment apparatus |
| US4687042A (en) * | 1986-07-23 | 1987-08-18 | Alumax, Inc. | Method of producing shaped metal parts |
| US4712413A (en) * | 1986-09-22 | 1987-12-15 | Alumax, Inc. | Billet heating process |
| FR2665654B1 (en) * | 1990-08-09 | 1994-06-24 | Armines | PRESSURE CASTING MACHINE OF A THIXOTROPIC METAL ALLOY. |
| CH683267A5 (en) * | 1991-06-10 | 1994-02-15 | Alusuisse Lonza Services Ag | A method for heating a workpiece of a metal alloy. |
| IT1278069B1 (en) * | 1994-05-17 | 1997-11-17 | Honda Motor Co Ltd | ALLOY MATERIAL FOR TISSOFUSION, PROCEDURE FOR THE PREPARATION OF SEMI-CAST ALLOY MATERIAL FOR TISSOFUSION AND PROCEDURE FOR |
| DE4420533A1 (en) * | 1994-06-14 | 1995-12-21 | Salzburger Aluminium Ag | Process for the production of castings from aluminum alloys |
| US5571346A (en) * | 1995-04-14 | 1996-11-05 | Northwest Aluminum Company | Casting, thermal transforming and semi-solid forming aluminum alloys |
| US5758707A (en) * | 1995-10-25 | 1998-06-02 | Buhler Ag | Method for heating metallic body to semisolid state |
| FR2746414B1 (en) * | 1996-03-20 | 1998-04-30 | Pechiney Aluminium | THIXOTROPE ALUMINUM-SILICON-COPPER ALLOY FOR SHAPING IN SEMI-SOLID CONDITION |
| FR2747327B1 (en) * | 1996-04-11 | 1998-06-12 | Pechiney Recherche | METHOD AND TOOL FOR HIGH SPEED SPINNING OF ALUMINUM ALLOYS AND PROFILE OBTAINED |
| EP0839589A1 (en) | 1996-11-04 | 1998-05-06 | Alusuisse Technology & Management AG | Method for producing a metallic profiled strand |
| WO2005101536A1 (en) * | 2004-04-06 | 2005-10-27 | Massachusetts Institute Of Technology (Mit) | Improving thermoelectric properties by high temperature annealing |
| CN103103401B (en) * | 2012-12-11 | 2016-04-20 | 芜湖恒坤汽车部件有限公司 | A kind of smelting preparation method of anti-surrender aluminium alloy extrusions |
| CN103103398B (en) * | 2012-12-11 | 2016-06-08 | 芜湖恒坤汽车部件有限公司 | A kind of smelting preparation method of resistant to rust aluminium alloy extrusions |
| CN103103415B (en) * | 2012-12-11 | 2016-06-08 | 芜湖恒坤汽车部件有限公司 | A kind of smelting preparation method of aluminium alloy extrusions |
| CN103103414B (en) * | 2012-12-11 | 2016-05-18 | 芜湖恒坤汽车部件有限公司 | A kind of chromaking is processed the smelting preparation method of aluminium alloy extrusions |
| CN103103416B (en) * | 2012-12-11 | 2016-12-07 | 黄娜茹 | A kind of smelting preparation method of heat insulated shape bar of aluminum alloy |
| CN103103399B (en) * | 2012-12-11 | 2016-06-08 | 芜湖恒坤汽车部件有限公司 | A kind of smelting preparation method of the aluminium alloy extrusions of good stability |
| CN103103402B (en) * | 2012-12-11 | 2016-05-18 | 芜湖恒坤汽车部件有限公司 | The smelting preparation method of a kind of static material end spraying aluminium alloy extrusions |
| CN103103413B (en) * | 2012-12-11 | 2016-06-08 | 芜湖恒坤汽车部件有限公司 | A kind of smelting preparation method of high-strength aluminum alloy section |
Family Cites Families (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CA957180A (en) * | 1971-06-16 | 1974-11-05 | Massachusetts, Institute Of Technology | Alloy compositions containing non-dendritic solids and process for preparing and casting same |
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1974
- 1974-04-04 LU LU69788A patent/LU69788A1/xx unknown
-
1975
- 1975-02-27 FR FR7506954A patent/FR2266749B1/fr not_active Expired
- 1975-02-27 FR FR7506953A patent/FR2266748B1/fr not_active Expired
- 1975-04-01 SU SU752125297A patent/SU722494A3/en active
- 1975-04-02 IT IT21921/75A patent/IT1034783B/en active
- 1975-04-02 DD DD185170A patent/DD117372A5/xx unknown
- 1975-04-02 DD DD185168A patent/DD117486A5/xx unknown
- 1975-04-02 DE DE2514355A patent/DE2514355C3/en not_active Expired
- 1975-04-02 ES ES436217A patent/ES436217A1/en not_active Expired
- 1975-04-02 IT IT21922/75A patent/IT1034784B/en active
- 1975-04-02 ES ES436216A patent/ES436216A1/en not_active Expired
- 1975-04-02 SE SE7503775A patent/SE7503775L/en unknown
- 1975-04-02 NO NO75751115A patent/NO141943C/en unknown
- 1975-04-02 DE DE19752514386 patent/DE2514386B2/en active Granted
- 1975-04-02 IL IL47001A patent/IL47001A/en unknown
- 1975-04-02 SE SE7503776A patent/SE420801B/en not_active IP Right Cessation
- 1975-04-02 NO NO751114A patent/NO141942C/en unknown
- 1975-04-03 CA CA223,752A patent/CA1045783A/en not_active Expired
- 1975-04-03 CA CA223,751A patent/CA1047223A/en not_active Expired
- 1975-04-03 BE BE155030A patent/BE827496A/en not_active IP Right Cessation
- 1975-04-03 GB GB13649/75A patent/GB1502114A/en not_active Expired
- 1975-04-03 GB GB13650/75A patent/GB1499934A/en not_active Expired
- 1975-04-03 JP JP4077775A patent/JPS5615455B2/ja not_active Expired
- 1975-04-03 JP JP4077675A patent/JPS5615454B2/ja not_active Expired
- 1975-04-03 NL NLAANVRAGE7503992,A patent/NL182415C/en not_active IP Right Cessation
- 1975-04-03 CH CH421375A patent/CH603805A5/xx not_active IP Right Cessation
- 1975-04-03 NL NLAANVRAGE7503994,A patent/NL182416C/en active Search and Examination
- 1975-04-03 CH CH411275A patent/CH602928A5/xx not_active IP Right Cessation
- 1975-04-03 IL IL47002A patent/IL47002A/en unknown
- 1975-04-03 BE BE155031A patent/BE827497A/en not_active IP Right Cessation
- 1975-04-04 ZA ZA00752150A patent/ZA752150B/en unknown
- 1975-04-04 ZA ZA00752151A patent/ZA752151B/en unknown
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