EP1458898B1 - Method of fabrication of an aluminium alloy article by hot- and cold-forming - Google Patents
Method of fabrication of an aluminium alloy article by hot- and cold-forming Download PDFInfo
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- EP1458898B1 EP1458898B1 EP02787956A EP02787956A EP1458898B1 EP 1458898 B1 EP1458898 B1 EP 1458898B1 EP 02787956 A EP02787956 A EP 02787956A EP 02787956 A EP02787956 A EP 02787956A EP 1458898 B1 EP1458898 B1 EP 1458898B1
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 5
- 238000004519 manufacturing process Methods 0.000 title description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 17
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 claims abstract description 17
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 17
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 15
- 239000010703 silicon Substances 0.000 claims abstract description 15
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 12
- 229910052735 hafnium Inorganic materials 0.000 claims abstract description 12
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims abstract description 12
- 239000011777 magnesium Substances 0.000 claims abstract description 12
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 12
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 11
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract description 11
- 239000010949 copper Substances 0.000 claims abstract description 11
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 10
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 239000011651 chromium Substances 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 9
- 239000011572 manganese Substances 0.000 claims abstract description 9
- 239000011701 zinc Substances 0.000 claims abstract description 9
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 8
- 229910052742 iron Inorganic materials 0.000 claims abstract description 7
- 239000010936 titanium Substances 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 4
- 238000000034 method Methods 0.000 claims description 25
- 229910045601 alloy Inorganic materials 0.000 claims description 20
- 239000000956 alloy Substances 0.000 claims description 20
- 239000011265 semifinished product Substances 0.000 claims description 17
- 239000002994 raw material Substances 0.000 claims description 7
- 238000000137 annealing Methods 0.000 claims description 6
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 239000000470 constituent Substances 0.000 claims description 2
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 abstract description 5
- 229910052782 aluminium Inorganic materials 0.000 abstract description 5
- 239000000203 mixture Substances 0.000 abstract description 5
- 239000002244 precipitate Substances 0.000 abstract description 3
- 239000013078 crystal Substances 0.000 abstract description 2
- 239000004411 aluminium Substances 0.000 abstract 1
- 229910021338 magnesium silicide Inorganic materials 0.000 abstract 1
- YTHCQFKNFVSQBC-UHFFFAOYSA-N magnesium silicide Chemical compound [Mg]=[Si]=[Mg] YTHCQFKNFVSQBC-UHFFFAOYSA-N 0.000 abstract 1
- 238000001953 recrystallisation Methods 0.000 description 11
- 238000005260 corrosion Methods 0.000 description 8
- 230000007797 corrosion Effects 0.000 description 8
- 238000005242 forging Methods 0.000 description 5
- 238000010438 heat treatment Methods 0.000 description 4
- 239000000243 solution Substances 0.000 description 4
- 229910019752 Mg2Si Inorganic materials 0.000 description 2
- 238000000265 homogenisation Methods 0.000 description 2
- 230000002401 inhibitory effect Effects 0.000 description 2
- 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 description 2
- 239000000463 material Substances 0.000 description 2
- 238000004881 precipitation hardening Methods 0.000 description 2
- 229910000789 Aluminium-silicon alloy Inorganic materials 0.000 description 1
- 208000032544 Cicatrix Diseases 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 241001396014 Priacanthus arenatus Species 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- -1 aluminum-silicon-magnesium Chemical compound 0.000 description 1
- 238000004873 anchoring Methods 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 230000029142 excretion Effects 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 239000003112 inhibitor Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 239000011159 matrix material Substances 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 231100000241 scar Toxicity 0.000 description 1
- 230000037387 scars Effects 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- 239000004575 stone Substances 0.000 description 1
- 238000005728 strengthening Methods 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 229910052845 zircon Inorganic materials 0.000 description 1
- GFQYVLUOOAAOGM-UHFFFAOYSA-N zirconium(iv) silicate Chemical compound [Zr+4].[O-][Si]([O-])([O-])[O-] GFQYVLUOOAAOGM-UHFFFAOYSA-N 0.000 description 1
Images
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon 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
- C22C21/02—Alloys based on aluminium with silicon 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Definitions
- the invention relates a method for Production of an aluminum component according to claim and a Component produced by a method according to claims 1-8.
- High strength Cu e.g., Al Mg Si 1 Cu 0.5
- Zn-containing have heat-treated Al semi-finished and Al forgings Although high static strength values, but is their Breaking strain low. In the case of notch effect (e.g. Rockfall) thus results in a low dynamic Strength.
- these alloys are vulnerable Corrosion, so that to avoid notch-acting Corrosion scars require expensive corrosion protection is.
- forged Al chassis parts are always exposed to stone chips (notches) and corrosion, In these areas, only in exceptional cases are Cu / Zn ambience Al materials used.
- Ductilers or notch-oriented Al Mg Si 1 alloys such as. B. the EN-AW 6082 are indeed because of their very low Cu and Zn content Corrosion resistant, but achieve this Alloys do not have sufficient strength values.
- German Offenlegungsschriften DE OS 2 103 614 and DE OS 2 213 136 each describe an aluminum-silicon-magnesium Alloy, the recrystallization inhibiting reacts, but these alloys are too low Strength on, also is the tendency to recrystallization this alloy for multi-formed or cold-formed Components still too high. The same goes for the known alloy according to EN-AW 6082.
- the object of the invention is a component and a method for producing a component to provide better than the prior art recrystallization-inhibiting effect and to a higher Strength and corrosion resistance of the components lead.
- the solution of the task consists in one Method according to Claim 1 and in a component according to claim 9.
- the Alloy a silicon content between 0.9 and 1.7 wt.% on.
- the invention is also characterized by the fact that the Alloy elements manganese, chrome and zirconium and / or Hafnium together account for at least 0.4% by weight exhibit. Preferably, the proportion of these Elements higher than 0.6% by weight. These elements act as Recrystallization inhibitors.
- the alloy has a silicon content of 0.9 to 1.3% on. It turned out that a lower Silicon content not to the required strength values leads.
- the silicon works in combination with the magnesium in the form of precipitation hardening (heat treatment), the in the form of Mg2Si precipitates. higher Levels of manganese and chromium also lead to one Precipitation hardening or strengthening.
- the alloy is particularly resistant to Recrystallization both in hot working and in Cold forming. It is almost independent of a high strength and a manufacturing process low tendency to corrosion.
- the low Corrosion tendency is mainly due to the low proportion of Attributed to copper and zinc.
- the process is characterized by the fact that cast Raw material of the alloy at temperatures between 420 ° C and 540 ° C, preferably homogenized between 460 ° C and 500 ° C becomes. During this homogenization, the Alloy components magnesium and silicon fine in the Aluminum matrix also distributes the form Dispersoids, as described, based on zirconium or hafnium, manganese, chromium and / or iron.
- the raw material Homogenizing for at least 4 hours is particularly preferred a homogenization of 12 h applied.
- the Semifinished between 500 ° C and 560 ° C, wherein each of the The highest possible temperature to choose is around To avoid recrystallisation nuclei.
- the semi-finished products will be if necessary, separated into workpieces suitable for forming and either one or several cold formed or possibly several times warm to components or more Reshaped semi-finished products.
- a machining of the Semi-finished products, z. B. by turning or milling is also appropriate.
- Hot or cold forming or cutting Editing can be done within the skill of the art take place and optionally conventional heat treatments include.
- the hot forming of the semifinished product follows at temperatures that are in the range of the usual solution annealing (between 440 ° C and 560 ° C). It is during the reshaping in particular during several forming steps make sure that the Temperature of the workpiece is not below the mentioned Temperature drops, resulting in coarse precipitates in the component structure would result.
- the forming process replaces the Process step of the solution annealing, which affects considerably the process costs and the duration of the process.
- the forming temperatures according to the invention are higher than the usual Forming temperatures, resulting in less solidification and thus a lower Rekristallisationskeimön in Microstructure causes.
- the recrystallization becomes sustainable suppressed.
- Higher strength values and above all significantly higher elongation at break in highly formed areas are the consequence.
- the workpiece After forming, the workpiece is preferably in water quenched, which freezes the structure. At the subsequent hot curing between 160 ° C and 240 ° C the desired strength increase takes place.
- the aluminum component according to the invention produced by a method according to any one of claims 1-8, in one of Alloy information corresponding composition one Tensile strength of at least 400 MPa and a minimum Elongation at break (A5) of 10%.
- Such components are preferably as tie rods or other chassis parts, Profiles, bolts, screws or wheels used.
- the Tension struts are quenched in water and at 200 ° C for 4 h artificially aged.
- the tie rods point both in the area a middle brace as well as in the area of a big eye, due to the high degree of deformation usually one having high degree of recrystallization, a Tensile strength of more than 400 MPa and a breaking elongation (A5) of more than 13%.
Abstract
Description
Die Erfindung betrifft ein Verfahren zur Herstellung eines Aluminiumbauteils nach Anspruch und ein Bauteil, hergestellt durch ein Verfahren nach Ansprüchen 1-8.The invention relates a method for Production of an aluminum component according to claim and a Component produced by a method according to claims 1-8.
Hochfeste Cu- (z.B. Al Mg Si 1 Cu 0,5) oder Zn-haltige, wärmebehandelte Al-Halbzeuge und Al-Schmiedeteile haben zwar hohe statische Festigkeitswerte, jedoch ist deren Bruchdehnung niedrig. Im Fall von Kerbwirkung (z.B. Steinschlag) resultiert somit eine geringe dynamische Festigkeit. Auch sind diese Legierungen anfällig gegenüber Korrosion, so dass zur Vermeidung kerbwirkender Korrosionsnarben ein teurer Korrosionsschutz erforderlich ist. Da z.B. hoch belastete, geschmiedete Al-Fahrwerksteile immer Steinschlag- (Kerben) und Korrosion ausgesetzt sind, werden in diesen Bereichen nur in Ausnahmefällen Cu-/Znhaltige Al-Werkstoffe eingesetzt. Duktilere bzw. kerbunempfinlichere Al Mg Si 1-Legierungen wie z. B. die EN-AW 6082 sind zwar wegen ihres sehr geringen Cu- und Zn-Gehaltes korrosionsbeständig, jedoch erreichen diese Legierungen keine ausreichende Festigkeitswerte.High strength Cu (e.g., Al Mg Si 1 Cu 0.5) or Zn-containing, have heat-treated Al semi-finished and Al forgings Although high static strength values, but is their Breaking strain low. In the case of notch effect (e.g. Rockfall) thus results in a low dynamic Strength. Also, these alloys are vulnerable Corrosion, so that to avoid notch-acting Corrosion scars require expensive corrosion protection is. As e.g. heavily loaded, forged Al chassis parts are always exposed to stone chips (notches) and corrosion, In these areas, only in exceptional cases are Cu / Znhaltige Al materials used. Ductilers or notch-oriented Al Mg Si 1 alloys such as. B. the EN-AW 6082 are indeed because of their very low Cu and Zn content Corrosion resistant, but achieve this Alloys do not have sufficient strength values.
Ein weiterer Nachteil derartiger Legierungen besteht darin, dass beim Umformen und späteren Wärmebehandeln hoch umgeformte Schmiede- und Halbzeugzonen grobkörnig rekristallisieren. Ein grobkörniges bzw. sprödes und minder festes Gefüge führt zu einem frühen Ausfall des Al-Bauteiles.Another disadvantage of such alloys is that that during forming and later heat treatment high Formed forging and semi-finished zones coarse-grained recrystallize. A coarse-grained or brittle and less firm structure leads to an early failure of the Al component.
Dies gilt vor allem dann, wenn z. B. zu Erzielung einer hohen Materialausbeute eine Mehrfachumformung beim Schmieden erforderlich ist. Bei der Mehrfachumformung erfolgt meist der höchste Umformungsgrad erst am Ende des Umformprozesses und somit bei Temperaturen zwischen 390°C und 450°C, so dass das Gefüge beim späteren Wärmebehandeln rekristallisiert. Noch problematischer ist das Rekristallisationsverhalten kalt umgeformter Al-Halbzeuge, die später wärmebehandelt werden. So wird z.B. für das Herstellen hoch fester Al-Schrauben kalt gezogener Draht oder Stangen verwendet, der dann über Stauchen und Pressen zu einem Schraubenrohling kalt umgeformt wird. Beim späteren Wärmebehandeln ist somit das Gefüge hoch rekristallisationsanfällig. Dasselbe gilt für kalt geschmiedete Al-Räder.This is especially true if z. B. to achieve a high material yield a Mehrfachumformung when Forging is required. In the multiple forming usually the highest degree of deformation occurs only at the end of the Forming process and thus at temperatures between 390 ° C and 450 ° C, allowing the microstructure to heat later recrystallized. Even more problematic is the recrystallization behavior cold-formed Al semi-finished products, later be heat treated. For example, for making high solid Al screws cold drawn wire or rods used, then about upsetting and pressing to a Screw blank is cold formed. Later Heat treatment is thus the structure high rekristallisationsanfällig. The same applies to cold forged Al wheels.
Die deutschen Offenlegungsschriften DE OS 2 103 614 und DE OS 2 213 136 beschreiben jeweils eine Aluminium-Silizium-Magnesium -Legierung, die rekristallisationshemmend reagiert, diese Legierungen weisen jedoch eine zu geringe Festigkeit auf, zudem ist die Neigung zur Rekristallisation dieser Legierung für mehrfachumgeformte oder kaltumgeformte Bauteile immer noch zu hoch. Das selbe gilt für die bekannte Legierung nach der EN-AW 6082.German Offenlegungsschriften DE OS 2 103 614 and DE OS 2 213 136 each describe an aluminum-silicon-magnesium Alloy, the recrystallization inhibiting reacts, but these alloys are too low Strength on, also is the tendency to recrystallization this alloy for multi-formed or cold-formed Components still too high. The same goes for the known alloy according to EN-AW 6082.
Die Aufgabe der Erfindung besteht darin, ein Bauteil und ein Verfahren zur Herstellung eines Bauteils bereitzustellen, die gegenüber dem Stand der Technik besser rekristallisationshemmend wirken und zu einer höheren Festigkeit und Korrosionsbeständigkeit der Bauteile führen. The object of the invention is a component and a method for producing a component to provide better than the prior art recrystallization-inhibiting effect and to a higher Strength and corrosion resistance of the components lead.
Die Lösung der Aufgabe besteht in einem Verfahren nach Anspruch 1 und in einem Bauteil nach Anspruch 9.The solution of the task consists in one Method according to Claim 1 and in a component according to claim 9.
Das erfindungsgemäße Bauteil oder Halbzeug hergestellt durch ein Verfahren nach einem der Ansprüche 1-8 besteht aus einer Aluminiumlegierung mit folgender Zusammensetzung:
- Silizium 0,9 - 1,3,
- Magnesium 0,7 - 1,2,
- Mangan 0, 5 - 1,0,
- Kupfer kleiner 0,1,
- Eisen kleiner 0,5,
- Chrom kleiner 0,25,
- Zirkon und/oder Hafnium 0,05 - 0,2.
- Kupfer kleiner 0,05,
- Eisen 0, 1 - 0,5,
- Chrom 0,05 - 0,2,
- Zink kleiner 0,05.
- Silicon 0.9 - 1.3,
- Magnesium 0.7 - 1.2,
- Manganese 0, 5 - 1.0,
- Copper smaller 0.1,
- Iron less than 0.5,
- Chrome smaller than 0.25,
- Zirconium and / or hafnium 0.05-0.2.
- Copper smaller 0.05,
- Iron 0, 1 - 0.5,
- Chromium 0.05 - 0.2,
- Zinc less than 0.05.
Zudem kann die Legierung, die Elemente
- Zink kleiner 0,2
- Titan kleiner 0,1
- Zinc less than 0.2
- Titanium less than 0.1
In einer vorteilhaften Ausgestaltungsform weist die Legierung einen Siliziumanteil zwischen 0,9 und 1,7 Gew.% auf.In an advantageous embodiment, the Alloy a silicon content between 0.9 and 1.7 wt.% on.
Die Erfindung zeichnet sich zudem dadurch aus, dass die Legierungselemente Mangan, Chrom und Zirkon und/oder Hafnium zusammen einen Anteil von mindestens 0,4 Gew. % aufweisen. In bevorzugter Weise liegt der Anteil dieser Elemente höher als 0,6 Gew. %. Diese Elemente fungieren als Rekristallisationshemmer.The invention is also characterized by the fact that the Alloy elements manganese, chrome and zirconium and / or Hafnium together account for at least 0.4% by weight exhibit. Preferably, the proportion of these Elements higher than 0.6% by weight. These elements act as Recrystallization inhibitors.
Diese Elemente bilden mit dem Aluminium beim Homogenisierungsglühen intermetallische Dispersoide, die die Korngrenzen verankern und sich auch während weiterer Temperaturbehandlungen nicht oder nur im geringen Masse wieder auflösen. Durch die Verankerung der Dispersoide an den Korngrenzen wird das Wachstum der Körner zu Grobkorn verhindert, wodurch somit die Rekristallisation nachhaltige unterdrückt wird. Zirkon und hafniumhaltige Dispersoide sind besonders temperaturstabil, was sich hemmend auf die Rekristallisation bei hohen Temperaturen auswirkt.These elements form with the aluminum at Homogenizing annealing intermetallic dispersoids, the anchor the grain boundaries and also during further Temperature treatments are not or only to a limited extent dissolve again. By anchoring the dispersoids At the grain boundaries, the growth of grains becomes coarse grain prevents, thus making the recrystallization sustainable is suppressed. Zirconium and hafnium-containing dispersoids are particularly temperature stable, which inhibits the Recrystallization at high temperatures affects.
Die Legierung weist einen Siliziumanteil von 0,9 bis 1,3 % auf. Es hat sich herausgestellt, dass ein niedrigerer Siliziumanteil nicht zu den geforderten Festigkeitswerten führt. Das Silizium wirkt in Kombination mit dem Magnesium in Form einer Ausscheidungshärtung (Wärmebehandlung), die sich in Form von Mg2Si-Ausscheidungen einstellt. Höhere Gehalte an Mangan und Chrom führen ebenfalls zu einer Ausscheidungshärtung bzw. Festigungssteigerung.The alloy has a silicon content of 0.9 to 1.3% on. It turned out that a lower Silicon content not to the required strength values leads. The silicon works in combination with the magnesium in the form of precipitation hardening (heat treatment), the in the form of Mg2Si precipitates. higher Levels of manganese and chromium also lead to one Precipitation hardening or strengthening.
Darüber hinaus ist es zweckmäßig, dass für eine Mischkristallhärtung, also einer Bildung von AlSi-Mischkristallen ein Überschuss an Silizium besteht, der nicht in Mg2Si-Ausscheidungen gebunden ist. Das Verhältnis von Silizium zu Magnesium liegt somit bevorzugt zwischen 1,1 bis 1,3 zu 1, besonders bevorzugt zwischen 1,16 bis 1,24 zu 1.In addition, it is appropriate for a Solid-solution hardening, ie formation of AlSi mixed crystals there is an excess of silicon, the is not bound in Mg2Si excretions. The relationship from silicon to magnesium is thus preferred between 1.1 to 1.3 to 1, more preferably between 1.16 to 1.24 to 1.
Die Legierung ist besonders resistent gegen Rekristallisation sowohl bei Warmumformung als auch bei Kaltumformung. Sie weist an sich nahezu unabhängig von einem Herstellungsverfahren eine hohe Festigkeit und eine geringe Korrosionsneigung auf. Die geringe Korrosionsneigung ist vor allem auf den geringen Anteil an Kupfer und Zink zurückzuführen.The alloy is particularly resistant to Recrystallization both in hot working and in Cold forming. It is almost independent of a high strength and a manufacturing process low tendency to corrosion. The low Corrosion tendency is mainly due to the low proportion of Attributed to copper and zinc.
Das Verfahren zeichnet sich dadurch aus, dass gegossenes Rohmaterial der Legierung bei Temperaturen zwischen 420° C und 540°C, bevorzugt zwischen 460°C und 500°C homogenisiert wird. Während dieser Homogenisierung werden die Legierungsbestandteile Magnesium und Silizium fein in der Aluminium-Matrix verteilt zudem bilden sich die Dispersoide, die, wie beschrieben, auf Basis vom Zirkon oder Hafnium, Mangan, Chrom und/oder Eisen bestehen.The process is characterized by the fact that cast Raw material of the alloy at temperatures between 420 ° C and 540 ° C, preferably homogenized between 460 ° C and 500 ° C becomes. During this homogenization, the Alloy components magnesium and silicon fine in the Aluminum matrix also distributes the form Dispersoids, as described, based on zirconium or hafnium, manganese, chromium and / or iron.
Es hat sich als vorteilhaft herausgestellt, das Rohmaterial mindestens 4 h zu homogenisieren, besonders bevorzugt wird eine Homogenisierung von 12 h angewendet.It has turned out to be advantageous, the raw material Homogenizing for at least 4 hours is particularly preferred a homogenization of 12 h applied.
Im weiteren Verfahren wird das Rohmaterial bei einer Temperatur zwischen 450° C und 560° C zu Halbzeugen geformt (z. B. Strangpressen oder Walzen von Blechen) und gegebenenfalls abgeschreckt. Bevorzugt erfolgt die Halbzeugformung zwischen 500°C und 560°C, wobei jeweils die höchstmögliche Temperatur zu wählen ist um Rekristallisationskeime zu vermeiden. Die Halbzeuge werden falls notwendig in umformgerechte Werkstücke vereinzelt und entweder ein- oder mehrfach kalt umgeformt oder gegebenenfalls mehrfach warm zu Bauteilen oder weiteren Halbzeugen umgeformt. Eine spanende Bearbeitung der Halbzeuge, z. B. durch Drehen oder Fräsen ist ebenfalls zweckmäßig. Das Warm- oder Kaltumformen oder das spanende Bearbeiten kann im Rahmen des fachmännischen Könnens erfolgen und gegebenenfalls übliche Wärmebehandlungen beinhalten.In the further process, the raw material at a Temperature formed between 450 ° C and 560 ° C to semi-finished products (eg extrusion or rolling of sheets) and optionally quenched. Preferably, the Semifinished between 500 ° C and 560 ° C, wherein each of the The highest possible temperature to choose is around To avoid recrystallisation nuclei. The semi-finished products will be if necessary, separated into workpieces suitable for forming and either one or several cold formed or possibly several times warm to components or more Reshaped semi-finished products. A machining of the Semi-finished products, z. B. by turning or milling is also appropriate. Hot or cold forming or cutting Editing can be done within the skill of the art take place and optionally conventional heat treatments include.
Das Warmumformen des Halbzeugs folgt bei Temperaturen, die im Bereich des üblichen Lösungsglühen liegen (zwischen 440°C und 560°C). Es ist während des Umformens insbesondere während mehrerer Umformschritte darauf zu achten, dass die Temperatur des Werkstücks nicht unter die genannte Temperatur fällt, was grobe Ausscheidungen im Bauteilgefüge zur Folge hätte. Der Umformvorgang ersetzt demnach den Prozessschritt des Lösungsglühens, was sich erheblich auf die Prozesskosten und die Prozessdauer auswirkt.The hot forming of the semifinished product follows at temperatures that are in the range of the usual solution annealing (between 440 ° C and 560 ° C). It is during the reshaping in particular during several forming steps make sure that the Temperature of the workpiece is not below the mentioned Temperature drops, resulting in coarse precipitates in the component structure would result. The forming process replaces the Process step of the solution annealing, which affects considerably the process costs and the duration of the process.
Die erfindungsgemäßen Umformtemperaturen, die gleichzeitig ein Lösungsglühen beinhalten, liegen höher als die üblichen Umformtemperaturen, was eine geringere Verfestigung und somit eine geringere Rekristallisationskeimbildung im Gefüge bewirkt. Somit wird die Rekristallisation nachhaltig unterdrückt. Höhere Festigkeitswerte und vor allem deutliche höhere Bruchdehnung in hochumgeformten Bereiche sind die Folge.The forming temperatures according to the invention, the same time a solution annealing, are higher than the usual Forming temperatures, resulting in less solidification and thus a lower Rekristallisationskeimbildung in Microstructure causes. Thus, the recrystallization becomes sustainable suppressed. Higher strength values and above all significantly higher elongation at break in highly formed areas are the consequence.
Nach dem Umformen wird das Werkstück bevorzugt in Wasser abgeschreckt, wodurch das Gefüge eingefroren wird. Beim anschließenden Warmaushärten zwischen 160°C und 240°C erfolgt die gewünschte Festigkeitssteigerung.After forming, the workpiece is preferably in water quenched, which freezes the structure. At the subsequent hot curing between 160 ° C and 240 ° C the desired strength increase takes place.
Das erfindungsgemäße Aluminiumbauteil hergestellt durch ein Verfahren nach einem der Ansprüche 1-8 weist bei einer der Legierungsangaben entsprechenden Zusammensetzung eine Zugfestigkeit von mindestens 400 MPa und eine minimale Bruchdehnung (A5) von 10 % auf. Derartige Bauteile werden bevorzugt als Zugstreben oder andere Fahrwerksteile, Profile, Bolzen, Schrauben oder Räder verwendet.The aluminum component according to the invention produced by a method according to any one of claims 1-8, in one of Alloy information corresponding composition one Tensile strength of at least 400 MPa and a minimum Elongation at break (A5) of 10%. Such components are preferably as tie rods or other chassis parts, Profiles, bolts, screws or wheels used.
Im Folgenden wird die Erfindung an Hand von zwei Beispielen näher erläutert. Das den Beispielen 1 und 2 zugrundeliegende Verfahrensschema ist in Fig. 1 dargestellt.In the following the invention is based on two examples explained in more detail. That the examples 1 and 2 The underlying process scheme is shown in FIG. 1 shown.
Eine Legierungsschmelze mit der Zusammensetzung in Gewicht %:
- Silizium 1,2,
- Magnesium 1,0,
- Mangan 0,5,
- Kupfer 0,05,
- Eisen 0,2,
- Chrom 0,2,
- Titan 0,05,
- Zink 0,1,
- Zirkon 0,2,
- Silicon 1,2,
- Magnesium 1.0,
- Manganese 0.5,
- Copper 0.05,
- Iron 0.2,
- Chrome 0.2,
- Titanium 0.05,
- Zinc 0.1,
- Zircon 0.2,
Die Werkstücke werden auf eine Temperatur von 530° C erhitzt und in mehreren Schmiedeprozessen (=Umformen) zu Zugstreben umgeformt. Während des Schmiedens fällt die Temperatur des Werkstückes nicht unter 440°C. Die Zugstreben werden in Wasser abgeschreckt und bei 200°C 4 h warmausgelagert. Die Zugstreben weisen sowohl im Bereich einer Mittelstrebe als auch im Bereich eines großen Auges, das auf Grund des hohen Umformgrades üblicherweise einen hohen Grad an Rekristallisation aufweist, eine Zugfestigkeit von mehr als 400 MPa und eine Bruchdehnung (A5) von mehr als 13 % auf.The workpieces are heated to a temperature of 530 ° C heated and in several forging processes (= forming) too Tension struts transformed. During forging, the falls Temperature of the workpiece not lower than 440 ° C. The Tension struts are quenched in water and at 200 ° C for 4 h artificially aged. The tie rods point both in the area a middle brace as well as in the area of a big eye, due to the high degree of deformation usually one having high degree of recrystallization, a Tensile strength of more than 400 MPa and a breaking elongation (A5) of more than 13%.
Analog Beispiel 1 werden Gussbarren homogenisiert und anschließend bei einer Temperatur von 500°C zu Blechen (=Halbzeug) gewalzt. Aus den Blechen werden runde Werkstücke ausgestanzt und diese in mehreren Schritten kalt zu Rädern umgeformt.As in Example 1, ingots are homogenized and then at a temperature of 500 ° C to sheets (= Semi-finished product) rolled. From the sheets are round Workpieces punched out and these cold in several steps transformed into wheels.
Claims (11)
- Process for producing a component or semi-finished product from an aluminium alloy, the alloy containing (in % by weight):silicon 0.9 - 1.3magnesium 0.7 - 1.2copper less than 0.1iron less than 0.5chromium less than 0.25zirconium and/or hafnium 0.05 - 0.2manganese 0.5 - 1.0
and the total amount of chromium and manganese and zirconium and/or hafnium is at least 0.6% by weight, in which processa cast raw material is homogenized at a temperature of between 420°C and 540°C,is shaped into semi-finished products at a temperature of between 450°C and 560°C,the semi-finished product is then heated to a solution annealing temperature of between 440°C and 560°C,is hot-formed one or more times at this temperature,the workpiece obtained in this way is quenched in water or in air, andis hot age-hardened at a temperature of between 160°C and 240°C. - Process for producing a component or semi-finished product from an aluminium alloy, the alloy containing (in % by weight):silicon 0.9 - 1.7magnesium 0.7 - 1.2copper less than 0.1iron less than 0.5chromium less than 0.25zirconium and/or hafnium 0.05 - 0.2manganese 0.5 - 1.0
and the total amount of chromium and manganese and zirconium and/or hafnium is at least 0.6% by weight, in which processa cast raw material is homogenized at a temperature of between 420°C and 540°C,is shaped into semi-finished products at a temperature of between 450°C and 560°C,the semi-finished product is then heated to a solution annealing temperature of between 440°C and 560°C,is hot-formed one or more times at this temperature,the workpiece obtained in this way is quenched in water or in air, andis hot age-hardened at a temperature of between 160°C and 240°C. - Process according to Claim 1 or 2, characterized in that the alloy additionally includes the following constituents, in % by weight:titanium less than 0.1zinc less than 0.2.
- Process according to one of Claims 1 to 3, characterized in that the ratio of silicon to magnesium is between 1.1 to 1 and 1.3 to 1.
- Process according to Claim 4, characterized in that the ratio of silicon to magnesium is between 1.16 to 1 and 1.24 to 1.
- Process according to one of Claims 1 to 5, characterized in that zirconium- and/or hafnium-containing dispersoids are anchored at the grain boundaries of the microstructure.
- Process according to one of Claims 1 to 6, characterized in that the cast raw material is homogenized for at least four hours.
- Process according to one of Claims 1 to 7, characterized in that the cast raw material is homogenized for twelve hours.
- Component produced by a process according to one of Claims 1 to 8.
- Component or semi-finished products as described in one of Claims 1 to 6, characterized in that the component has an elongation at break A5 of more than 10%.
- Component or semi-finished product as described in one of Claims 1 to 7, characterized in that the component or semi-finished product is an underbody part, in particular a tension strut or a bolt, a profiled section, a screw or a wheel.
Applications Claiming Priority (3)
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DE10163039 | 2001-12-21 | ||
DE10163039A DE10163039C1 (en) | 2001-12-21 | 2001-12-21 | Hot and cold formable component made of an aluminum alloy and process for its production |
PCT/EP2002/014452 WO2003054243A1 (en) | 2001-12-21 | 2002-12-18 | Hot- and cold-formed aluminium alloy |
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EP1458898A1 EP1458898A1 (en) | 2004-09-22 |
EP1458898B1 true EP1458898B1 (en) | 2005-04-27 |
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EP02787956A Expired - Lifetime EP1458898B1 (en) | 2001-12-21 | 2002-12-18 | Method of fabrication of an aluminium alloy article by hot- and cold-forming |
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US (2) | US20050095167A1 (en) |
EP (1) | EP1458898B1 (en) |
AT (1) | ATE294252T1 (en) |
AU (1) | AU2002352255A1 (en) |
DE (2) | DE10163039C1 (en) |
ES (1) | ES2239261T3 (en) |
WO (1) | WO2003054243A1 (en) |
Cited By (1)
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EP2644725A2 (en) | 2012-03-30 | 2013-10-02 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy forged material for automobile and method for manufacturing the same |
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DE102005060297A1 (en) * | 2005-11-14 | 2007-05-16 | Fuchs Kg Otto | Energieabsorbtionsbauteil |
JP4944525B2 (en) * | 2006-07-18 | 2012-06-06 | 株式会社神戸製鋼所 | Bolt manufacturing method, bolt, bolt profile, bolt molding apparatus, and bolt profile molding method |
DE102007032143A1 (en) * | 2007-07-09 | 2009-01-15 | Thyssenkrupp Drauz Nothelfer Gmbh | Motor vehicle door, has inner panel and reinforcement brackets integrally formed, and frame-shaped component comprising reinforcement regions, where frame shaped component is hot-formed from high-strength steel plate |
EP2149618B1 (en) | 2008-07-30 | 2011-10-26 | Olab S.r.l. | Hot pressing process, particularly for providing metal unions for pneumatic, hydraulic and fluid-operated circuits, and metal union obtained thereby |
DE102009059804A1 (en) | 2009-12-21 | 2011-06-22 | Daimler AG, 70327 | Method for producing and increasing strength of a composite component, which is formed from a cast component made of an aluminum alloy, comprises connecting the cast component over a bolted connection |
EP2787094B1 (en) * | 2011-12-02 | 2016-12-07 | UACJ Corporation | Aluminum alloy material and aluminum alloy structure and production process therefor |
WO2014003074A1 (en) | 2012-06-27 | 2014-01-03 | 株式会社Uacj | Aluminum alloy sheet for blow molding and production method therefor |
JP6557476B2 (en) * | 2015-02-10 | 2019-08-07 | 三菱アルミニウム株式会社 | Aluminum alloy fin material |
SI24911A (en) | 2016-03-04 | 2016-07-29 | Impol 2000, d.d. | High-strength aluminum alloy Al-Mg-Si and procedure for its manufacture |
US20190136348A1 (en) * | 2016-06-01 | 2019-05-09 | Aleris Aluminum Duffel Bvba | 6xxx-series aluminium alloy forging stock material and method of manufacturing thereof |
WO2019139723A1 (en) | 2018-01-12 | 2019-07-18 | Accuride Corporation | Aluminum alloys for applications such as wheels and methods of manufacture |
FR3101641B1 (en) * | 2019-10-04 | 2022-01-21 | Constellium Issoire | Aluminum alloy precision sheets |
CN112522552B (en) * | 2020-11-04 | 2022-04-26 | 佛山科学技术学院 | Corrosion-resistant aluminum alloy and preparation method and application thereof |
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US3945860A (en) * | 1971-05-05 | 1976-03-23 | Swiss Aluminium Limited | Process for obtaining high ductility high strength aluminum base alloys |
CA962172A (en) * | 1971-05-05 | 1975-02-04 | Olin Corporation | High ductility high strength aluminum base alloys and process for obtaining same |
US3717512A (en) * | 1971-10-28 | 1973-02-20 | Olin Corp | Aluminum base alloys |
CH624147A5 (en) * | 1976-12-24 | 1981-07-15 | Alusuisse | |
JPS58156197A (en) * | 1982-03-10 | 1983-09-17 | Sumitomo Light Metal Ind Ltd | Super high pressure plate fin type heat exchanger |
FR2529578B1 (en) * | 1982-07-02 | 1986-04-11 | Cegedur | METHOD FOR IMPROVING BOTH FATIGUE RESISTANCE AND TENACITY OF HIGH RESISTANCE AL ALLOYS |
FR2617188B1 (en) * | 1987-06-23 | 1989-10-20 | Cegedur | AL-BASED ALLOY FOR CASING AND PROCESS FOR OBTAINING |
US5108519A (en) * | 1988-01-28 | 1992-04-28 | Aluminum Company Of America | Aluminum-lithium alloys suitable for forgings |
JPH03287738A (en) * | 1990-04-03 | 1991-12-18 | Kobe Steel Ltd | Fin material for heat exchanger assembled by vacuum brazing method and its manufacture |
DE4421744C2 (en) * | 1993-07-02 | 1996-05-23 | Fuchs Fa Otto | Use of a wrought alloy of the type AlMgSiCu for the production of high-strength and corrosion-resistant parts |
JPH07197219A (en) * | 1993-12-28 | 1995-08-01 | Furukawa Electric Co Ltd:The | Production of aluminum alloy sheet for forming |
FR2737225B1 (en) * | 1995-07-28 | 1997-09-05 | Pechiney Rhenalu | AL-CU-MG ALLOY WITH HIGH FLUID RESISTANCE |
FR2744136B1 (en) * | 1996-01-25 | 1998-03-06 | Pechiney Rhenalu | THICK ALZNMGCU ALLOY PRODUCTS WITH IMPROVED PROPERTIES |
JPH11310841A (en) * | 1998-04-28 | 1999-11-09 | Nippon Steel Corp | Aluminum alloy extruded shape excellent in fatigue strength, and its production |
US6630037B1 (en) * | 1998-08-25 | 2003-10-07 | Kobe Steel, Ltd. | High strength aluminum alloy forgings |
-
2001
- 2001-12-21 DE DE10163039A patent/DE10163039C1/en not_active Expired - Fee Related
-
2002
- 2002-12-18 DE DE50202955T patent/DE50202955D1/en not_active Expired - Lifetime
- 2002-12-18 AU AU2002352255A patent/AU2002352255A1/en not_active Abandoned
- 2002-12-18 ES ES02787956T patent/ES2239261T3/en not_active Expired - Lifetime
- 2002-12-18 WO PCT/EP2002/014452 patent/WO2003054243A1/en not_active Application Discontinuation
- 2002-12-18 AT AT02787956T patent/ATE294252T1/en not_active IP Right Cessation
- 2002-12-18 EP EP02787956A patent/EP1458898B1/en not_active Expired - Lifetime
- 2002-12-18 US US10/499,755 patent/US20050095167A1/en not_active Abandoned
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EP2644725A2 (en) | 2012-03-30 | 2013-10-02 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy forged material for automobile and method for manufacturing the same |
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Publication number | Publication date |
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DE10163039C1 (en) | 2003-07-24 |
ATE294252T1 (en) | 2005-05-15 |
US20050095167A1 (en) | 2005-05-05 |
WO2003054243A1 (en) | 2003-07-03 |
EP1458898A1 (en) | 2004-09-22 |
DE50202955D1 (en) | 2005-06-02 |
AU2002352255A1 (en) | 2003-07-09 |
US20080078480A1 (en) | 2008-04-03 |
ES2239261T3 (en) | 2005-09-16 |
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