CA2965738C - Ultra high strength 6xxx forged aluminium alloys - Google Patents
Ultra high strength 6xxx forged aluminium alloys Download PDFInfo
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- CA2965738C CA2965738C CA2965738A CA2965738A CA2965738C CA 2965738 C CA2965738 C CA 2965738C CA 2965738 A CA2965738 A CA 2965738A CA 2965738 A CA2965738 A CA 2965738A CA 2965738 C CA2965738 C CA 2965738C
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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
- C22F1/05—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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21C—MANUFACTURE OF METAL SHEETS, WIRE, RODS, TUBES OR PROFILES, OTHERWISE THAN BY ROLLING; AUXILIARY OPERATIONS USED IN CONNECTION WITH METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL
- B21C23/00—Extruding metal; Impact extrusion
- B21C23/001—Extruding metal; Impact extrusion to improve the material properties, e.g. lateral extrusion
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
- B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
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- 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
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- 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
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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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Forging (AREA)
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Abstract
The invention relates to an ultra-high strength 6xxx-series aluminium alloy forged product for structural components, produced by a process comprising steps: a) casting a 6xxx aluminium alloy billet with: Si; Fe; Cu; Mn; Mg; Cr; Zr; Zn; Ti, the reminder aluminium; b) homogenising the cast billet; c) quenching said homogenised billet; d) heating the homogenised and quenched billet of c); e) extruding said billet of d); f) quenching the extruded product; g) stretching the extruded product to obtain a plastic deformation; h) heating cut-to-length extruded rod to forging temperature; i) forging in heated mould; j) separate solutionising at a temperature between 2 minutes and 1 hour; k) water quenching the forged and solutionised material; 1) room temperature ageing for a duration up to 30 days; m) ageing to T6 temper for holding times ranging from 2 to 20 hours. The forged product having an ultimate tensile strength above 400 MPa.
Description
Ultra High Strength 6xxx Forged Aluminium Alloys [0001] The invention relates to ultra-high strength AA6xxx-series aluminium alloy forgings particularly suitable for automotive, rail or transportation structural components, exhibiting an ultimate tensile strength UTS typically higher than 400 MPa in T6 temper, preferably higher than 450 MPa, and excellent corrosion resistance.
More particularly such forgings are produced through a manufacturing process which, besides including subsequent extrusion and forging steps, includes multiple solutionising and quench steps /o in order to achieve, after ultimate age hardening, high strength and excellent corrosion resistance on Cu-doped AA6xxx-series alloys.
More particularly such forgings are produced through a manufacturing process which, besides including subsequent extrusion and forging steps, includes multiple solutionising and quench steps /o in order to achieve, after ultimate age hardening, high strength and excellent corrosion resistance on Cu-doped AA6xxx-series alloys.
[0002] Unless otherwise stated, all information concerning the chemical composition of the alloys is expressed as a percentage by weight based on the total weight of the alloy. "6xxx aluminium /5 alloy" or "6xxx alloy" designate an aluminium alloy having magnesium and silicon as major alloying elements. "AA6xxx-series aluminium alloy" designates any 6xxx aluminium alloy listed in "International Alloy Designations and Chemical Composition Limits for Wrought Aluminum and Wrought Aluminum Alloys" published by The Aluminum Association, Inc. Unless otherwise stated, the definitions of metallurgical tempers listed in the European standard EN 515 will apply.
20 Static tensile mechanical characteristics, in other words, the ultimate tensile strength R. (or UTS), the tensile yield strength at 0.2% plastic elongation Rp0,2 (or YTS), and elongation A% (or E%), are determined by a tensile test according to NF EN ISO 6892-1.
20 Static tensile mechanical characteristics, in other words, the ultimate tensile strength R. (or UTS), the tensile yield strength at 0.2% plastic elongation Rp0,2 (or YTS), and elongation A% (or E%), are determined by a tensile test according to NF EN ISO 6892-1.
[0003] Aluminium alloy compositions and tempers have been developed for obtaining satisfying 25 strength and corrosion behavior in car components such as chassis-suspension or body structure parts, but also rail or transportation structural components in particular when they are made from forgings obtained from extruded rough products.
In order to achieve tensile properties in excess of 400 MPa in 6xxx alloys, it is essential to maximise both the ageing response through an adequate solutionising of solute elements, predominantly Mg, 30 Si and Cu, while maximising retention of the fibrous structure through minimal recrystallisation.
Date Recue/Date Received 2022-12-14 Said recrystallisation is controlled through the addition of dispersoid elements, typically Mn, Cr and Zr and appropriate homogenisation temperatures. It is also controlled through alloy processing conditions, which arc defined so as to minimise stored-energy and thereby maximise rccrystallization temperature.
To achieve adequate solutionising, according to the prior art, highly alloyed 6xlm alloys are usually separately solutionised and quenched after the ultimate hot forming step (in this case forging). Such a solution can be found in the patent application EP 2548933 Al by "Nissan Motor Co". When alloys are strongly alloyed it is often required to apply an extended solutionising treatment (in excess of 90min) at high temperature (530-560 C) in order to achieve excellent solutionising. Such a case to is described in the patent application JP2012-097321 by "Furukawa Sky Aluminium-Corp". The corollary to this is that extended recrystal ization will occur on highly alloyed alloys (unless significant dispersoid additions are made) as they are brought to a fully solutionised temper and the additional strength gained by improved solutionising shall be mitigated by recovery and recrystallisation.
In order to achieve tensile properties in excess of 400 MPa in 6xxx alloys, it is essential to maximise both the ageing response through an adequate solutionising of solute elements, predominantly Mg, 30 Si and Cu, while maximising retention of the fibrous structure through minimal recrystallisation.
Date Recue/Date Received 2022-12-14 Said recrystallisation is controlled through the addition of dispersoid elements, typically Mn, Cr and Zr and appropriate homogenisation temperatures. It is also controlled through alloy processing conditions, which arc defined so as to minimise stored-energy and thereby maximise rccrystallization temperature.
To achieve adequate solutionising, according to the prior art, highly alloyed 6xlm alloys are usually separately solutionised and quenched after the ultimate hot forming step (in this case forging). Such a solution can be found in the patent application EP 2548933 Al by "Nissan Motor Co". When alloys are strongly alloyed it is often required to apply an extended solutionising treatment (in excess of 90min) at high temperature (530-560 C) in order to achieve excellent solutionising. Such a case to is described in the patent application JP2012-097321 by "Furukawa Sky Aluminium-Corp". The corollary to this is that extended recrystal ization will occur on highly alloyed alloys (unless significant dispersoid additions are made) as they are brought to a fully solutionised temper and the additional strength gained by improved solutionising shall be mitigated by recovery and recrystallisation.
[0004] The invention relates to forgings manufactured through a process including, besides subsequent extrusion and forging steps, multiple solutionising and quench steps, to achieve excellent solutionising and strong retention of the fibrous structure on 6xxx type alloys, achieving typically, after last step age hardening (T6 temper), an ultimate tensile strength UTS higher than 400 MPa, and preferably higher than 450 MPa, and an excellent corrosion resistance.
[0005] Solidus Ts is the temperature below which the alloy exhibits a solid fraction equal to 1.
Solvus defines the temperature, which is the limit of solid solubility in the equilibrium phase diagram of the alloy. For high strength requirements, eutectic alloying elements such as Si, Mg and Cu should be added to form precipitated hardening phases. IIowever, the addition of alloying elements generally results in a decrease in the difference between solidus and solvus temperatures.
When the content of eutectic alloying elements is higher than a critical value, the solidus to solvus range of the alloy becomes a narrow "window", with typically a solidus to solvus difference lower than 20 C, and consequently the solution heat treatment of the aforementioned elements usually achieved during extrusion cannot be obtained without observing incipient melting. Indeed local temperature gradients achieved during extrusion and forging, generally exceed 20 C implying that, as solvus is reached, parts of the product will display temperatures in excess of solidus Ts.
Solvus defines the temperature, which is the limit of solid solubility in the equilibrium phase diagram of the alloy. For high strength requirements, eutectic alloying elements such as Si, Mg and Cu should be added to form precipitated hardening phases. IIowever, the addition of alloying elements generally results in a decrease in the difference between solidus and solvus temperatures.
When the content of eutectic alloying elements is higher than a critical value, the solidus to solvus range of the alloy becomes a narrow "window", with typically a solidus to solvus difference lower than 20 C, and consequently the solution heat treatment of the aforementioned elements usually achieved during extrusion cannot be obtained without observing incipient melting. Indeed local temperature gradients achieved during extrusion and forging, generally exceed 20 C implying that, as solvus is reached, parts of the product will display temperatures in excess of solidus Ts.
[0006] According to the prior art, high strength forgings obtained from extruded rough products, and from 6xxx-series aluminium alloys characterised by a minimum Silicon content of 0.7 /o and
7 PCT/EP2015/075401 minimum Magnesium content of 0.6%, for example of the AA 6082, 6182, 6110, or 6056 type, are produced by:
a) casting one of the following aluminium alloys AA6082, 6110, 6182 or 6056 acc. to AA standard or to a restricted composition within AA standard;
b) homogenising, c) cooling to room temperature;
d) heating a homogenised cast billet to a temperature 50 C to 100 C lower than solidus temperature (approx. 575 C);
e) extruding said billet through a die to produce a solid section profile with an exit temperature to (typically 500 C) lower than solidus (typically 550 C), in order to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles;
f) cooling to room temperature;
g) stretching;
h) heating cut-to-length extruded rod to forging temperature (400-520 C);
i) forging in heated mould (150-350 C);
j) separate solutionising at 530-560 C for durations between 30 min. and 90 min.;
k) water quenching the forged material down to room temperature;
1) room temperature ageing m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
However, ultimate tensile strengths achieved with this processing route do not exceed 450MPa.
Generally speaking, 400MPa is a maximum especially when ageing has to be shifted away from peak ageing T66 in order to guarantee minimum elongation values higher than 10 %.
[00071 The applicant decided to develop a novel combination of 6xxx-series alloy and process which secures an ultimate tensile strength higher than 400 MPa, preferably higher than 450MPa, and even higher than 480 MPa.
a) casting one of the following aluminium alloys AA6082, 6110, 6182 or 6056 acc. to AA standard or to a restricted composition within AA standard;
b) homogenising, c) cooling to room temperature;
d) heating a homogenised cast billet to a temperature 50 C to 100 C lower than solidus temperature (approx. 575 C);
e) extruding said billet through a die to produce a solid section profile with an exit temperature to (typically 500 C) lower than solidus (typically 550 C), in order to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles;
f) cooling to room temperature;
g) stretching;
h) heating cut-to-length extruded rod to forging temperature (400-520 C);
i) forging in heated mould (150-350 C);
j) separate solutionising at 530-560 C for durations between 30 min. and 90 min.;
k) water quenching the forged material down to room temperature;
1) room temperature ageing m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
However, ultimate tensile strengths achieved with this processing route do not exceed 450MPa.
Generally speaking, 400MPa is a maximum especially when ageing has to be shifted away from peak ageing T66 in order to guarantee minimum elongation values higher than 10 %.
[00071 The applicant decided to develop a novel combination of 6xxx-series alloy and process which secures an ultimate tensile strength higher than 400 MPa, preferably higher than 450MPa, and even higher than 480 MPa.
[0008] A first object of the invention is an aluminium alloy forged product obtained by following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. A; Fe : < 0.5 wt. %; Cu: 0.1-1.5 wt. %; Mn: 0.4-1.0 wt. A;
Mg: 0.6-1.2 wt. A; Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. A; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TFI which is 5 C to 80 C
lower than solidus temperature Ts, typically TH in the range of 500-560 C, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said billet down to room temperature by using a first water quench system;
d) heating the homogenised billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
/o e) extruding said billet through a die to produce a solid section with an exit temperature (typically 530 C) lower than Ts (typically 550 C), in order to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles, and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
g) stretching the extruded product to obtain a plastic deformation typically between 0.5% and 10%, preferably up to 5%;
h) heating cut-to-length extruded rod to forging temperature, typically between 400 and 520 C;
i) forging in heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 min. and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours, and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. A; Fe : < 0.5 wt. %; Cu: 0.1-1.5 wt. %; Mn: 0.4-1.0 wt. A;
Mg: 0.6-1.2 wt. A; Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. A; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TFI which is 5 C to 80 C
lower than solidus temperature Ts, typically TH in the range of 500-560 C, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said billet down to room temperature by using a first water quench system;
d) heating the homogenised billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
/o e) extruding said billet through a die to produce a solid section with an exit temperature (typically 530 C) lower than Ts (typically 550 C), in order to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles, and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
g) stretching the extruded product to obtain a plastic deformation typically between 0.5% and 10%, preferably up to 5%;
h) heating cut-to-length extruded rod to forging temperature, typically between 400 and 520 C;
i) forging in heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 min. and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours, and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
[0009] According to the invention, the aluminium alloy extruded product is obtained by casting a billet from a 6xxx aluminium alloy comprising: Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. %; Cu: 0.1-1.5 wt. A;
Mn: 0.4-1.0 wt. A; Mg: 0.6-1.2 wt. A; Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt.
%; Zn: < 0.2 wt.%; Ti: <
0.2 wt.%, the rest being aluminium and inevitable impurities. The aluminium alloy according to the invention is of the AlMgSi type, which, compared with other such as e.g.
AlZnMg alloys, provides an excellent combination of high tensile strength and resistance to corrosion.
Date Recue/Date Received 2022-06-07 - 4a -[0009a] In accordance with one aspect there is provided an aluminium alloy forged product characterized in that the process to obtain the product comprises the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. A; Fe: < 0.5 wt. /0; Cu: 0.6-1.0 wt. A; Mn: 0.4-1.0 wt. A;
Mg: 0.7-1.2 wt. A;
Cr: 0.05-0.25 wt%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid io phases;
c) quenching said homogenised billet down to room temperature by using water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet of d) through a die to produce a solid section with an exit temperature lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
quenching the extruded product down to room temperature by using water quench system;
g) stretching the extruded product to obtain a plastic deformation;
h) heating cut-to-length extruded rod to forging temperature;
i) forging in heated mould between 150 and 350 C;
i) separate solutionising at a temperature between 530 and 560 C for durations between 2 minutes and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours;
and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
Date Recue/Date Received 2022-01-20 - 4h -[0009b] In accordance with another aspect there is provided a process for manufacturing an aluminium alloy forged product described herein comprising the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. /0; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. A;
Mg: 0.7-1.0 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid io phases;
c) quenching said homogenized billet down to room temperature by using water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet through a die to produce a solid section with an exit temperature lower than Ts lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using water quench system;
g) stretching the extruded product to obtain a plastic deformation;
h) heating cut-to-length extruded rod to forging temperature;
i) forging in heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 mm.
and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
Date Recue/Date Received 2022-01-20
Mn: 0.4-1.0 wt. A; Mg: 0.6-1.2 wt. A; Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt.
%; Zn: < 0.2 wt.%; Ti: <
0.2 wt.%, the rest being aluminium and inevitable impurities. The aluminium alloy according to the invention is of the AlMgSi type, which, compared with other such as e.g.
AlZnMg alloys, provides an excellent combination of high tensile strength and resistance to corrosion.
Date Recue/Date Received 2022-06-07 - 4a -[0009a] In accordance with one aspect there is provided an aluminium alloy forged product characterized in that the process to obtain the product comprises the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. A; Fe: < 0.5 wt. /0; Cu: 0.6-1.0 wt. A; Mn: 0.4-1.0 wt. A;
Mg: 0.7-1.2 wt. A;
Cr: 0.05-0.25 wt%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid io phases;
c) quenching said homogenised billet down to room temperature by using water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet of d) through a die to produce a solid section with an exit temperature lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
quenching the extruded product down to room temperature by using water quench system;
g) stretching the extruded product to obtain a plastic deformation;
h) heating cut-to-length extruded rod to forging temperature;
i) forging in heated mould between 150 and 350 C;
i) separate solutionising at a temperature between 530 and 560 C for durations between 2 minutes and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours;
and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
Date Recue/Date Received 2022-01-20 - 4h -[0009b] In accordance with another aspect there is provided a process for manufacturing an aluminium alloy forged product described herein comprising the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. /0; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. A;
Mg: 0.7-1.0 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid io phases;
c) quenching said homogenized billet down to room temperature by using water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet through a die to produce a solid section with an exit temperature lower than Ts lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using water quench system;
g) stretching the extruded product to obtain a plastic deformation;
h) heating cut-to-length extruded rod to forging temperature;
i) forging in heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 mm.
and 1 hour;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
Date Recue/Date Received 2022-01-20
[0010] The process according to the invention consists in particular in replacing conventional homogenising followed by slow cooling, heating and extruding followed again by slow cooling of AA6xxx alloy billets, by high temperature homogenising and quenching followed by heating, extruding and quenching again, and does not comprise a separate post-extrusion solution heat treatment, because, as a result of steps b) and c), most part of the alloying elements which contribute to the formation of hardening particles are in solid solution in the lattice of the extrudate.
[0011] The present invention therefore provides a process to manufacture a range of 6xxx alloys with superior mechanical properties, especially if applied to a sufficiently copper-doped AlMgSiCu, to with strength levels in excess of 400 MPa and even 450 or 480 MPa, hitherto not achieved through a conventional route. In addition, good extrudability and forgeability is maintained because the limitation with extrusion speed due to premature speed cracking resulting from incipient melting is minimised due to a higher level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases prior to extrusion.
[0012] According to the invention, a billet is provided resulting from casting a 6xxx aluminium alloy, ie. an aluminium alloy having magnesium and silicon as major alloying elements. Preferably, this aluminium alloy is a high-strength 6xxx aluminium alloy, such as AA6082, AA6182, AA6056, AA6110 or any copper-doped alloy derived from the said AA6xxx aluminium alloys.
[0013] This alloy has preferably a high Cu content, typically between 0.1 and 1.5 wt. Vo, more preferably between 0.4 and 1.2 wt. Vo, even more preferably between 0.6 and 1.0 wt. Vo. Dispersoid elements, Mn with a content of 0.4-1.0 wt. Vo, Cr with a content of 0.05-0.25 wt. % and Zr with a content of 0.05-0.2 wt. Vo, are added to control recrystallization and maximize the retention of fibrous structure of the extrudate and the forged component.
[0014] Si and Mg content are defined so as to ensure high level of dissolved Mg2Si while minimising presence of undissolved Mg2Si in the forged component after ultimate solutionising step, with a maximum content of 0.5 wt.%. For example, when solutionising at 550 C is applied at the ultimate step of the invention, the content of dissolved Mg is 0.623 wt.%, dissolved Si is 0.977 wt.% and undissolved Mg2Si 0.45wt.%.
[00151 Si is combined with Mg to form Mg2Si. The precipitation of Mg2Si contributes to increasing the strcngth of the final aluminium alloy forged product.
If the Si content is less than 0.7 wt.%, the final product does not have a sufficiently high strength, it means a tensile strength not higher than 400 MPa. If it is lower than 0.9 wt.%, tensile strength will be at most 450 MPa and with less than 1.1wt.% it will be lower than 480 MPa.
On the other hand, if the Si content is more than 1.3 wt.%, the level of undissolved Mg2Si is too high and extrudabi]ity is reduced as well as corrosion resistance and toughness of the resultant final forged product.
to [0016] Mg is combined with Si to form Mg2Si. Therefore Mg is indispensable for strengthening the product of the present invention. If the Mg content is lower than 0.7 wt.%, the effect is too weak. On the other hand, if the Mg content is higher than 1.2 wt.%, the billet becomes difficult to be extruded and the extruded bar to be forged. Moreover, a large amount of Mg2Si particles tends to precipitate during quenching process after the solution treatment. In addition, the Mg content is preferably between 0.7 wt.% and 1.1 wt.% and more preferably between 0.8 wt.% and 1.0 wt.%.
[0017] Fe is an impurity and combines with other elements to form intermetallic compounds.
These precipitated particles lower fracture toughness and fatigue strength of the final forged product. Especially, if the Fe content is higher than 0.5 wt.% it is difficult to obtain an aluminium alloy forged product with both high strength and high toughness as required for automotive structure and suspension applications. Preferably, its content is lower than or equal to 0.3 wt.%
and more preferably, lower than or equal to 0.2 wt.%.
[0018] Mn also combines with Al to form intermetallic compounds which control recrystallisation. However, if the Mn content is less than 0.4 wt.%, the effect is not sufficient. On the other hand, if the content of Mn is higher than 1.0 wt.%, coarse precipitated particles are formed and both the workability and the toughness of the aluminium alloy are reduced. The Mn content is preferably between 0.5 wt.% and 0.9 wt.% and more preferably between 0.5 wt.% and 0.7 wt.%.
[0019] The cast billet according to the invention is homogenised for a duration between 2 and 10 hours at a temperature between 5 C and 80 C lower than solidus, and then water quenched.
[0020] The homogenised and quenched cast billet to be extruded is heated to a soaking temperature Th below the solidus temperature Ts, between Ts-5 C and Ts-125 C.
For example, solidus temperature is near 575 C for alloys AA6082 and AA6182. The billets are preferably heated and held at the soaking temperature during ten seconds to several minutes.
[00211 The billet is then introduced in the extrusion press and extruded through a die to form a solid extruded product or extrudate. The extrusion speed is controlled to have an extrudate surface exit temperature lower than solidus temperature Ts, respectively 530 and 550 C
approximately.
The exit temperature should be high enough to merely avoid precipitation.
Practically, the targeted to extrudate surface temperature is commonly ranging from 530 C to 550 C, to have an extrusion speed compatible with a satisfying productivity and avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles. The extrusion ratio (starting cross-sectional area divided by final cross-sectional area) is at least 8 to maximize the fibrous structure of the extrudate.
[0022] The extruded product is then water quenched at the exit of the extrusion press, i.e. in an area located between 500 mm and 5 m of the exit from the die. It is cooled down to room temperature with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid on the extrudate.
[0023] The extrudate is then stretched to obtain a plastic deformation typically between 0.5%
and 10%, preferably up to 5%, in order to have stress-relieved straight profiles.
[0024] The extruded bar is then cut to length, heated to forging temperature, typically between 400 and 520 C, and then forged in a heated mould typically between 150 and 350 C.
10025] After forging, parts undergo a separate solutionising at a temperature between 530 and 560 C for a duration comprised between 2 min. and 1 hour and then water quenched with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid, down to room temperature.
The product is then aged at room temperature for a duration between 6 hours and 30 days , after which artificial ageing is applied to achieve T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
[0026] The process according to the invention allows to obtain forged products made from Cu-doped 6xxx alloys, which were until now very difficult to solutionise because of their very narrow solv-us-solidus temperature window and the risk of recrystallization during ultimate separate solutionising prior to final age-hardening treatment. The process and chemical composition of the invention permits to obtain a forged product displaying a near to fully wrought structure by to retaining the wrought structure generated during extrusion in parts of the forged component submitted to limited or no deformation during forging and by limiting the extent of recrystallization occurring during the ultimate separate solutionising step. This process is particularly well suited to alloys with Mg2Si content comprised between 1.2 wt. % and 1.6 wt. %, Si excess up to 0.7%, particularly if comprised between 0.2 wt. % and 0.7 wt. %, and especially if copper content lies between 0.4 wt.% and 1.5 wt.%, which gives a solv-us to solidus temperature difference approximately equal to or even lower than 10 C, and renders such alloy almost impossible to extrude when processed according to the prior art route.
[0027] As this alloy comprises, further to Mn, additional dispersoid elements zirconium, between 0.05 and 0.2 wt. %, and Cr, between 0.05 and 0.25 wt. %, the microstructures of the extrudates show a strong fibrous retention providing an additional strengthening contribution, considered important in meeting such high mechanical property values. After having applied the process according to the invention to Cu doped AlMgSiCu aluminium alloys, the applicant was able to obtain forged components having at T6 temper ultimate tensile strengths higher than 450 MPa, even higher than 480 MPa.
[0028] Mechanical properties achieved in T6 temper on invention forgings after manufacturing according to the aforementioned process were significantly higher than by using conventional process on AA 6082 and displayed a far higher tolerance to solutionising conditions i.e. increased ease of solutionising at low temperature and soaking time and high resistance to recrystallization.
[00291 Moreover a forged product manufactured according to the invention also displays a limited sensitivity to intergranular corrosion as assessed according to ISO
11846B and opposed to what the copper level would lead a corrosion expert to expect.
[00301 Such forged products arc particularly suitable as automotive body structure or chassis-suspension parts and especially suspension arms.
EXAMPLE
[0031] Forged suspension arms were made from two 6xxx aluminium alloys, the first one being of the AA6082 type, the other one according to the invention, starting from extruded round bars with a diameter of 40 mm.
to Said bars were extruded by following two different process routes: the current prior art route for AA6082 alloys and the route according to the invention for others.
The chemical compositions of these alloys are shown on Table I in weight %.
Si Fe Cu Mn Mg Cr Ni Zn Ti Pb V Zr AA6082 1.112 0.197 0.061 0.744 0.807 0.193 0.003 0.012 0.029 0.001 Invention 1.3 0.16 0.74 0.53 0.89 0.1 0.04 0.008 0.019 0.0011 0.011 0.13 Table I
I Iomogenised cast billets having a diameter of 308 mm and a length of 1200 mm were heated, introduced into an extrusion press and pressed to form 40 mm in diameter bars.
Forged suspension arms were obtained by following a conventional route for AA6082 alloys:
a) homogenising the cast billet at a temperature TH close to 480 C, for a duration of 5 hours;
b) cooling said billet down to room temperature;
c) heating the homogenised billet to a temperature Th close to 500 C;
c) extruding said billet through a die to produce round bars with an exit temperature close to 530 C;
d) cooling the extruded product down to room temperature;
e) stretching the extruded product to obtain a plastic deformation close to 1%;
f) heating cut-to-length extruded rod to forging temperature, close to 500 C;
g) forging in mould heated close to 300 C;
h) separate solutionising at a temperature close to 530 C for 30 min.;
i) water quenching the forged material with an intense cooling device down to room temperature;
j) room temperature ageing for a duration of 1 day;
k) ageing to T6 temper by a one-step heat treatment at 175 C for 8 hours.
Forged suspension arms were obtained by following the route according to the invention for other ones ("Invention"):
a) homogenising the cast billet at a temperature TH close to 520 C, for a duration of 5 hours;
b) quenching said billet down to room temperature by using water quench system;
c) heating the homogenised billet to a temperature Th close to 500 C;
d) extruding said billet through a die to produce round bars with an exit temperature close to to 530 C;
e) quenching the extruded product down to room temperature by using water quench system;
f) stretching the extruded product to obtain a plastic deformation close to 1%;
g) heating cut-to-length extruded rod to forging temperature close to 500 C;
h) forging in heated mould close to 300 C;
i) separate solutionising at a temperature close to 550 C for 30 min.;
j) quenching the forged material with an intense cooling device down to room temperature;
k) room temperature ageing for a duration of lday;
1) ageing to T6 temper by a one-step heat treatment at 170 C for 8 hours.
[0032] Tensile test specimens were machined in the suspension arms. Table 2 shows the ultimate tensile strength (u-Ts), the yield strength (YS) and the elongation of forged products.
Rm Rp0,2 A
Alloy Solutionising Ageing Temper [MPa] [MPa] ryd AA 6082 530 C/30 min. 175 C/8h T6 378 358 11 AA 6082 530 C/30 min. 175 C/8h T6 376 354 12.5 Invention 550 C/30 min. 170 C/8h T6 481 452 13 Invention 550 C/30 min. 170 C/8h T6 484 456 12 Table 2 [0033] The results of table 2 show that the process routc according to the invention enables the manufacture of aluminium alloy forged products having significantly higher strength (UTS and YS) than products obtained by a conventional route, and similar elongation.
[0034] Corrosion tests were performed using the ISO 11846B test for 24 hours of exposure time on suspension arms as above, the ones obtained from AA6082 alloy following the prior art route, the other ones according to the invention.
[0035] Figure 1 shows no significant difference for products according to the invention, with a maximum surface attack depth of 310 microns and a maximum end grain attack depth of 380 microns for the product according to the invention compared to respectively 390 and and 320 microns for AA6082 alloys processed through a prior art route.
[0036] These results show that the process route according to the invention enables the manufacture of aluminium alloy extruded products having simultaneously better strength (UTS
and YS) and equivalent corrosion resistance than products obtained by a conventional route.
[00151 Si is combined with Mg to form Mg2Si. The precipitation of Mg2Si contributes to increasing the strcngth of the final aluminium alloy forged product.
If the Si content is less than 0.7 wt.%, the final product does not have a sufficiently high strength, it means a tensile strength not higher than 400 MPa. If it is lower than 0.9 wt.%, tensile strength will be at most 450 MPa and with less than 1.1wt.% it will be lower than 480 MPa.
On the other hand, if the Si content is more than 1.3 wt.%, the level of undissolved Mg2Si is too high and extrudabi]ity is reduced as well as corrosion resistance and toughness of the resultant final forged product.
to [0016] Mg is combined with Si to form Mg2Si. Therefore Mg is indispensable for strengthening the product of the present invention. If the Mg content is lower than 0.7 wt.%, the effect is too weak. On the other hand, if the Mg content is higher than 1.2 wt.%, the billet becomes difficult to be extruded and the extruded bar to be forged. Moreover, a large amount of Mg2Si particles tends to precipitate during quenching process after the solution treatment. In addition, the Mg content is preferably between 0.7 wt.% and 1.1 wt.% and more preferably between 0.8 wt.% and 1.0 wt.%.
[0017] Fe is an impurity and combines with other elements to form intermetallic compounds.
These precipitated particles lower fracture toughness and fatigue strength of the final forged product. Especially, if the Fe content is higher than 0.5 wt.% it is difficult to obtain an aluminium alloy forged product with both high strength and high toughness as required for automotive structure and suspension applications. Preferably, its content is lower than or equal to 0.3 wt.%
and more preferably, lower than or equal to 0.2 wt.%.
[0018] Mn also combines with Al to form intermetallic compounds which control recrystallisation. However, if the Mn content is less than 0.4 wt.%, the effect is not sufficient. On the other hand, if the content of Mn is higher than 1.0 wt.%, coarse precipitated particles are formed and both the workability and the toughness of the aluminium alloy are reduced. The Mn content is preferably between 0.5 wt.% and 0.9 wt.% and more preferably between 0.5 wt.% and 0.7 wt.%.
[0019] The cast billet according to the invention is homogenised for a duration between 2 and 10 hours at a temperature between 5 C and 80 C lower than solidus, and then water quenched.
[0020] The homogenised and quenched cast billet to be extruded is heated to a soaking temperature Th below the solidus temperature Ts, between Ts-5 C and Ts-125 C.
For example, solidus temperature is near 575 C for alloys AA6082 and AA6182. The billets are preferably heated and held at the soaking temperature during ten seconds to several minutes.
[00211 The billet is then introduced in the extrusion press and extruded through a die to form a solid extruded product or extrudate. The extrusion speed is controlled to have an extrudate surface exit temperature lower than solidus temperature Ts, respectively 530 and 550 C
approximately.
The exit temperature should be high enough to merely avoid precipitation.
Practically, the targeted to extrudate surface temperature is commonly ranging from 530 C to 550 C, to have an extrusion speed compatible with a satisfying productivity and avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot-spots but still allowing to dissolve part of the constituent particles. The extrusion ratio (starting cross-sectional area divided by final cross-sectional area) is at least 8 to maximize the fibrous structure of the extrudate.
[0022] The extruded product is then water quenched at the exit of the extrusion press, i.e. in an area located between 500 mm and 5 m of the exit from the die. It is cooled down to room temperature with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid on the extrudate.
[0023] The extrudate is then stretched to obtain a plastic deformation typically between 0.5%
and 10%, preferably up to 5%, in order to have stress-relieved straight profiles.
[0024] The extruded bar is then cut to length, heated to forging temperature, typically between 400 and 520 C, and then forged in a heated mould typically between 150 and 350 C.
10025] After forging, parts undergo a separate solutionising at a temperature between 530 and 560 C for a duration comprised between 2 min. and 1 hour and then water quenched with an intense cooling device, for example a device projecting sprayed water or a water based cooling liquid, down to room temperature.
The product is then aged at room temperature for a duration between 6 hours and 30 days , after which artificial ageing is applied to achieve T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
[0026] The process according to the invention allows to obtain forged products made from Cu-doped 6xxx alloys, which were until now very difficult to solutionise because of their very narrow solv-us-solidus temperature window and the risk of recrystallization during ultimate separate solutionising prior to final age-hardening treatment. The process and chemical composition of the invention permits to obtain a forged product displaying a near to fully wrought structure by to retaining the wrought structure generated during extrusion in parts of the forged component submitted to limited or no deformation during forging and by limiting the extent of recrystallization occurring during the ultimate separate solutionising step. This process is particularly well suited to alloys with Mg2Si content comprised between 1.2 wt. % and 1.6 wt. %, Si excess up to 0.7%, particularly if comprised between 0.2 wt. % and 0.7 wt. %, and especially if copper content lies between 0.4 wt.% and 1.5 wt.%, which gives a solv-us to solidus temperature difference approximately equal to or even lower than 10 C, and renders such alloy almost impossible to extrude when processed according to the prior art route.
[0027] As this alloy comprises, further to Mn, additional dispersoid elements zirconium, between 0.05 and 0.2 wt. %, and Cr, between 0.05 and 0.25 wt. %, the microstructures of the extrudates show a strong fibrous retention providing an additional strengthening contribution, considered important in meeting such high mechanical property values. After having applied the process according to the invention to Cu doped AlMgSiCu aluminium alloys, the applicant was able to obtain forged components having at T6 temper ultimate tensile strengths higher than 450 MPa, even higher than 480 MPa.
[0028] Mechanical properties achieved in T6 temper on invention forgings after manufacturing according to the aforementioned process were significantly higher than by using conventional process on AA 6082 and displayed a far higher tolerance to solutionising conditions i.e. increased ease of solutionising at low temperature and soaking time and high resistance to recrystallization.
[00291 Moreover a forged product manufactured according to the invention also displays a limited sensitivity to intergranular corrosion as assessed according to ISO
11846B and opposed to what the copper level would lead a corrosion expert to expect.
[00301 Such forged products arc particularly suitable as automotive body structure or chassis-suspension parts and especially suspension arms.
EXAMPLE
[0031] Forged suspension arms were made from two 6xxx aluminium alloys, the first one being of the AA6082 type, the other one according to the invention, starting from extruded round bars with a diameter of 40 mm.
to Said bars were extruded by following two different process routes: the current prior art route for AA6082 alloys and the route according to the invention for others.
The chemical compositions of these alloys are shown on Table I in weight %.
Si Fe Cu Mn Mg Cr Ni Zn Ti Pb V Zr AA6082 1.112 0.197 0.061 0.744 0.807 0.193 0.003 0.012 0.029 0.001 Invention 1.3 0.16 0.74 0.53 0.89 0.1 0.04 0.008 0.019 0.0011 0.011 0.13 Table I
I Iomogenised cast billets having a diameter of 308 mm and a length of 1200 mm were heated, introduced into an extrusion press and pressed to form 40 mm in diameter bars.
Forged suspension arms were obtained by following a conventional route for AA6082 alloys:
a) homogenising the cast billet at a temperature TH close to 480 C, for a duration of 5 hours;
b) cooling said billet down to room temperature;
c) heating the homogenised billet to a temperature Th close to 500 C;
c) extruding said billet through a die to produce round bars with an exit temperature close to 530 C;
d) cooling the extruded product down to room temperature;
e) stretching the extruded product to obtain a plastic deformation close to 1%;
f) heating cut-to-length extruded rod to forging temperature, close to 500 C;
g) forging in mould heated close to 300 C;
h) separate solutionising at a temperature close to 530 C for 30 min.;
i) water quenching the forged material with an intense cooling device down to room temperature;
j) room temperature ageing for a duration of 1 day;
k) ageing to T6 temper by a one-step heat treatment at 175 C for 8 hours.
Forged suspension arms were obtained by following the route according to the invention for other ones ("Invention"):
a) homogenising the cast billet at a temperature TH close to 520 C, for a duration of 5 hours;
b) quenching said billet down to room temperature by using water quench system;
c) heating the homogenised billet to a temperature Th close to 500 C;
d) extruding said billet through a die to produce round bars with an exit temperature close to to 530 C;
e) quenching the extruded product down to room temperature by using water quench system;
f) stretching the extruded product to obtain a plastic deformation close to 1%;
g) heating cut-to-length extruded rod to forging temperature close to 500 C;
h) forging in heated mould close to 300 C;
i) separate solutionising at a temperature close to 550 C for 30 min.;
j) quenching the forged material with an intense cooling device down to room temperature;
k) room temperature ageing for a duration of lday;
1) ageing to T6 temper by a one-step heat treatment at 170 C for 8 hours.
[0032] Tensile test specimens were machined in the suspension arms. Table 2 shows the ultimate tensile strength (u-Ts), the yield strength (YS) and the elongation of forged products.
Rm Rp0,2 A
Alloy Solutionising Ageing Temper [MPa] [MPa] ryd AA 6082 530 C/30 min. 175 C/8h T6 378 358 11 AA 6082 530 C/30 min. 175 C/8h T6 376 354 12.5 Invention 550 C/30 min. 170 C/8h T6 481 452 13 Invention 550 C/30 min. 170 C/8h T6 484 456 12 Table 2 [0033] The results of table 2 show that the process routc according to the invention enables the manufacture of aluminium alloy forged products having significantly higher strength (UTS and YS) than products obtained by a conventional route, and similar elongation.
[0034] Corrosion tests were performed using the ISO 11846B test for 24 hours of exposure time on suspension arms as above, the ones obtained from AA6082 alloy following the prior art route, the other ones according to the invention.
[0035] Figure 1 shows no significant difference for products according to the invention, with a maximum surface attack depth of 310 microns and a maximum end grain attack depth of 380 microns for the product according to the invention compared to respectively 390 and and 320 microns for AA6082 alloys processed through a prior art route.
[0036] These results show that the process route according to the invention enables the manufacture of aluminium alloy extruded products having simultaneously better strength (UTS
and YS) and equivalent corrosion resistance than products obtained by a conventional route.
Claims (25)
1. An aluminium alloy forged product characterized in that the process to obtain the product comprises the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. %; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. %; Mg:
0.7-1.2 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said homogenised billet down to room temperature by using a first water quench systern;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet of d) through a die to produce a solid section with an exit temperature lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
stretching the extruded product to obtain a plastic deformation;
h) heating a cut-to-length extruded rod to forging temperature;
i) forging the cut-to-length extruded rod in a heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 minutes and 1 hour producing a forged and solutionised material;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours;
and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. %; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. %; Mg:
0.7-1.2 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said homogenised billet down to room temperature by using a first water quench systern;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet of d) through a die to produce a solid section with an exit temperature lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
stretching the extruded product to obtain a plastic deformation;
h) heating a cut-to-length extruded rod to forging temperature;
i) forging the cut-to-length extruded rod in a heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 minutes and 1 hour producing a forged and solutionised material;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours;
and the aluminium alloy forged product ultimate tensile strength is higher than 400 MPa.
2) An aluminium alloy forged product according to claim 1 characterised in that in b) the TH is in the range of 500-560 C.
3) An aluminium alloy forged product according to claim 1 or 2 characterised in that the exit temperature of e) is 530 C.
4) An aluminium alloy forged product according to any one of claims 1 to 3 characterised in that the Ts is 550 C.
5) An aluminium alloy forged product according to any one of claims 1 to 4 characterised in that in g) the plastic deformation is between 0.5% and 10%.
6) An aluminium alloy forged product according to any one of claims 1 to 4 characterised in that in g) the plastic deformation is up to 5%.
7) An aluminium alloy forged product according to any one of claims 1 to 6 characterised in that in h) the forging temperature is between 400 and 520 C.
8) An aluminium alloy forged product according to any one of claims 1 to 7 characterised in that said 6xxx aluminium alloy comprises Si: 0.9-1.3 wt.
9) An aluminium alloy forged product according to claim 8 characterised in that said 6xxx aluminium alloy comprises Si: 1.1-1.3 wt.%.
10) An aluminium alloy forged product according to any one of claims 1 to 9 characterised in that said 6xxx aluminium alloy comprises Mn: 0.5-0.9 wt.%.
11) An aluminium alloy forged product according to claim 10 characterised in that said 6xxx aluminium alloy comprises Mn: 0.5-0.7 wt.%.
12) An aluminium alloy forged product according to any one of claims 1 to 11 characterised in that Fe < 0.3 wt. %.
13) An aluminium alloy forged product according to claim 12 characterised in that Fe < 0.2 wt. %.
14) An aluminium alloy forged product according to any one of claims 1 to 13 characterised in that the aluminium alloy forged product ultimate tensile strength is higher than 450MPa.
15) An aluminium alloy forged product according to claim 14 characterised in that the ultimate tensile strength is higher than 480 MPa.
16) An aluminium alloy forged product according to any one of claims 1 to 15 characterised in that the aluminium alloy forged product is an automotive body-structure part.
17) An aluminium alloy forged product according to any of claims 1 to 16 characterised in that the aluminium alloy forged product is an automotive chassis-suspension part.
18) An aluminium alloy forged product according to any of claims 1 to 16 characterised in that the aluminium alloy forged product is an automotive suspension arm.
19) A process for manufacturing an aluminium alloy forged product according to any one of claims 1 to 18 comprising the following steps:
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. %; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. %; Mg:
0.7-1.0 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said homogenized billet down to room temperature by using a first water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet through a die to produce a solid section with an exit temperature lower than Ts lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
stretching the extruded product to obtain a plastic deformation;
h) heating a cut-to-length extruded rod to forging temperature;
i) forging the cut-to-length extruded rod in a heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 min.
and 1 hour producing a forged and solutionised material;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
a) casting a billet from a 6xxx aluminium alloy comprising:
Si: 0.7-1.3 wt. %; Fe: < 0.5 wt. %; Cu: 0.6-1.0 wt. %; Mn: 0.4-1.0 wt. %; Mg:
0.7-1.0 wt. %;
Cr: 0.05-0.25 wt.%; Zr: 0.05-0.2 wt. %; Zn: < 0.2 wt.%; Ti: < 0.2 wt.% , the rest being aluminium and inevitable impurities;
b) homogenising the cast billet at a temperature TH which is 5 C to 80 C
lower than solidus temperature Ts, for a duration between 2 and 10 hours to ensure high level of dissolution of constituent particles while ensuring precipitation and controlled coarsening of dispersoid phases;
c) quenching said homogenized billet down to room temperature by using a first water quench system;
d) heating the homogenised and quenched billet to a temperature Th between (Ts ¨ 5 C) and (Ts - 125 C);
e) extruding said billet through a die to produce a solid section with an exit temperature lower than Ts lower than Ts, to avoid incipient melting due to non-equilibrium melting of eutectic phases in profile hot spots but still allowing to dissolve part of the constituent particles and with an extruding ratio of at least 8;
f) quenching the extruded product down to room temperature by using a second water quench system;
stretching the extruded product to obtain a plastic deformation;
h) heating a cut-to-length extruded rod to forging temperature;
i) forging the cut-to-length extruded rod in a heated mould between 150 and 350 C;
j) separate solutionising at a temperature between 530 and 560 C for durations between 2 min.
and 1 hour producing a forged and solutionised material;
k) water quenching the forged and solutionised material down to room temperature;
1) room temperature ageing for a duration between 6 hours and 30 days;
m) ageing to T6 temper by a one-or multiple-step heat treatment at temperatures ranging from 150 to 200 C for holding times ranging from 2 to 20 hours.
20) A process for manufacturing an aluminium alloy forged product according to claim 19 characterised in that in b) the TH is in the range of 500-560 C.
21) A process for manufacturing an aluminium alloy forged product claim 19 or 20 characterised in that the exit temperature of e) is 530 C.
22) A process for manufacnffing an aluminium alloy forged product according to any one of claims 19 to 21 characterised in that the Ts is 550 C.
23) A process for manufacturing an aluminium alloy forged product according to any one of claims 19 to 22 characterised in that in g) the plastic deformation is between 0.5%
and 10%
and 10%
24) A process for manufacturing an aluminium alloy forged product according to any one of claims 19 to 22 characterised in that in g) the plastic deformation is up to 5%.
25) A process for manufacturing an aluminium alloy forged product according to any one of claims 19 to 24 characterised in that in h) the forging temperature is between 400 and 520 C.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP14003717.7 | 2014-11-05 | ||
| EP14003717.7A EP3018226A1 (en) | 2014-11-05 | 2014-11-05 | Ultra high strength products forged from 6xxx aluminium alloys having excellent corrosion resistance |
| PCT/EP2015/075401 WO2016071257A1 (en) | 2014-11-05 | 2015-11-02 | Ultra high strength 6xxx forged aluminium alloys |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CA2965738A1 CA2965738A1 (en) | 2016-05-12 |
| CA2965738C true CA2965738C (en) | 2023-09-12 |
Family
ID=51865969
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA2965738A Active CA2965738C (en) | 2014-11-05 | 2015-11-02 | Ultra high strength 6xxx forged aluminium alloys |
Country Status (8)
| Country | Link |
|---|---|
| US (1) | US20170314113A1 (en) |
| EP (2) | EP3018226A1 (en) |
| CA (1) | CA2965738C (en) |
| HU (1) | HUE043253T2 (en) |
| MX (1) | MX2017005153A (en) |
| PL (1) | PL3215648T3 (en) |
| SI (1) | SI3215648T1 (en) |
| WO (1) | WO2016071257A1 (en) |
Families Citing this family (18)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3418409B1 (en) * | 2016-02-19 | 2020-04-01 | NHK Spring Co., Ltd. | Aluminum alloy and fastener member |
| WO2018037390A2 (en) | 2016-08-26 | 2018-03-01 | Shape Corp. | Warm forming process and apparatus for transverse bending of an extruded aluminum beam to warm form a vehicle structural component |
| EP3299482B1 (en) | 2016-09-21 | 2019-05-29 | Aleris Aluminum Duffel BVBA | Method of manufacturing a high-strength 6xxx-series forging material |
| US11072844B2 (en) | 2016-10-24 | 2021-07-27 | Shape Corp. | Multi-stage aluminum alloy forming and thermal processing method for the production of vehicle components |
| CN106938310B (en) * | 2017-03-23 | 2018-06-05 | 遵义航天新力精密铸锻有限公司 | The finish forge processing method of aviation aircraft connecting seat |
| EP3728666A1 (en) | 2017-12-21 | 2020-10-28 | Constellium Extrusion Decin S.r.o. | 6xxx aluminium alloy extruded forging stock and method of manufacturing thereof |
| CN108188192B (en) * | 2018-01-02 | 2019-09-10 | 龙口市丛林铝材有限公司 | A kind of big Wall-Thickness Difference multi-cavity aluminum profile lateral bending problem accurate control method of big specification |
| AT522376B1 (en) * | 2019-04-05 | 2022-03-15 | Hammerer Aluminium Ind Extrusion Gmbh | Aluminum-based alloy continuous casting billet, extruded profile and method of manufacturing the same |
| CN110408805B (en) * | 2019-04-10 | 2021-06-18 | 广东坚美铝型材厂（集团）有限公司 | Aluminum alloy bar and preparation method thereof |
| CN110129636A (en) * | 2019-05-29 | 2019-08-16 | 安徽生信铝业股份有限公司 | A kind of high-speed rail windscreen aluminium alloy and preparation method thereof |
| JP7380127B2 (en) | 2019-11-20 | 2023-11-15 | 株式会社レゾナック | Manufacturing method for aluminum alloy forgings for automobile suspension parts |
| JP7380134B2 (en) | 2019-11-27 | 2023-11-15 | 株式会社レゾナック | Manufacturing method for aluminum alloy forgings for automobile suspension parts |
| CN110885942B (en) * | 2019-12-17 | 2021-05-07 | 中铝材料应用研究院有限公司 | Medium-strength 7xxx series aluminum alloy plate suitable for hot stamping forming-quenching integrated process |
| CN110938765B (en) * | 2019-12-18 | 2022-02-22 | 东北轻合金有限责任公司 | Manufacturing method of high-strength Al-Mg-Si aluminum alloy bar for automobile chassis |
| EP3981893A1 (en) * | 2020-10-07 | 2022-04-13 | AMAG rolling GmbH | Plate made of a rolled aluminium alloy and production of such a plate |
| CN113088773A (en) * | 2021-03-05 | 2021-07-09 | 长春市吉通凯撒铝业有限责任公司 | High-strength aluminum alloy and production process and application thereof |
| CN115449652A (en) * | 2022-08-04 | 2022-12-09 | 广东伟业铝厂集团有限公司 | Special-shaped multi-cavity chassis profile for new energy automobile and preparation method thereof |
| CN115572871B (en) * | 2022-10-31 | 2023-09-15 | 山东骏程金属科技有限公司 | Commercial aluminum alloy forged wheel and preparation method thereof |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2004084058A (en) * | 2002-06-27 | 2004-03-18 | Kobe Steel Ltd | Method for producing aluminum alloy forging for transport structural material and aluminum alloy forging |
| JP4101614B2 (en) * | 2002-11-01 | 2008-06-18 | 住友軽金属工業株式会社 | Method for producing high-strength aluminum alloy extruded material with excellent resistance to corrosion and stress corrosion cracking |
| JP2004292937A (en) * | 2003-03-28 | 2004-10-21 | Kobe Steel Ltd | Aluminum alloy forging material for transport carrier structural material, and production method therefor |
| US8152940B2 (en) * | 2006-03-31 | 2012-04-10 | Kobe Steel, Ltd. | Aluminum alloy forging member and process for producing the same |
| JP5180496B2 (en) * | 2007-03-14 | 2013-04-10 | 株式会社神戸製鋼所 | Aluminum alloy forging and method for producing the same |
| WO2011114665A1 (en) | 2010-03-15 | 2011-09-22 | 日本化薬株式会社 | Heat-resistant adhesive |
| JP2012097321A (en) | 2010-11-02 | 2012-05-24 | Furukawa-Sky Aluminum Corp | High-strength aluminum alloy forged product excellent in stress corrosion cracking resistance and forging method for the same |
-
2014
- 2014-11-05 EP EP14003717.7A patent/EP3018226A1/en not_active Withdrawn
-
2015
- 2015-11-02 SI SI201530705T patent/SI3215648T1/en unknown
- 2015-11-02 EP EP15790515.9A patent/EP3215648B1/en active Active
- 2015-11-02 WO PCT/EP2015/075401 patent/WO2016071257A1/en active Application Filing
- 2015-11-02 MX MX2017005153A patent/MX2017005153A/en unknown
- 2015-11-02 US US15/522,808 patent/US20170314113A1/en not_active Abandoned
- 2015-11-02 HU HUE15790515A patent/HUE043253T2/en unknown
- 2015-11-02 PL PL15790515T patent/PL3215648T3/en unknown
- 2015-11-02 CA CA2965738A patent/CA2965738C/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| PL3215648T3 (en) | 2019-07-31 |
| EP3018226A1 (en) | 2016-05-11 |
| SI3215648T1 (en) | 2019-07-31 |
| EP3215648B1 (en) | 2019-01-23 |
| HUE043253T2 (en) | 2019-08-28 |
| MX2017005153A (en) | 2018-01-23 |
| WO2016071257A1 (en) | 2016-05-12 |
| CA2965738A1 (en) | 2016-05-12 |
| EP3215648A1 (en) | 2017-09-13 |
| US20170314113A1 (en) | 2017-11-02 |
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