EP2652163B1 - 7xxx alloy thick products and their process of manufacture - Google Patents
7xxx alloy thick products and their process of manufacture Download PDFInfo
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- EP2652163B1 EP2652163B1 EP11808242.9A EP11808242A EP2652163B1 EP 2652163 B1 EP2652163 B1 EP 2652163B1 EP 11808242 A EP11808242 A EP 11808242A EP 2652163 B1 EP2652163 B1 EP 2652163B1
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- 238000004519 manufacturing process Methods 0.000 title claims description 14
- 238000000034 method Methods 0.000 title claims description 14
- 229910045601 alloy Inorganic materials 0.000 title description 27
- 239000000956 alloy Substances 0.000 title description 27
- 229910052782 aluminium Inorganic materials 0.000 claims description 19
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 19
- 238000001816 cooling Methods 0.000 claims description 17
- 229910052749 magnesium Inorganic materials 0.000 claims description 16
- 229910052802 copper Inorganic materials 0.000 claims description 15
- 229910052726 zirconium Inorganic materials 0.000 claims description 15
- 229910052748 manganese Inorganic materials 0.000 claims description 14
- 229910052719 titanium Inorganic materials 0.000 claims description 14
- 238000005266 casting Methods 0.000 claims description 13
- 229910052742 iron Inorganic materials 0.000 claims description 13
- 239000000243 solution Substances 0.000 claims description 13
- 229910052804 chromium Inorganic materials 0.000 claims description 12
- 239000012535 impurity Substances 0.000 claims description 8
- 239000004411 aluminium Substances 0.000 claims description 7
- 230000006835 compression Effects 0.000 claims description 7
- 238000007906 compression Methods 0.000 claims description 7
- 238000010438 heat treatment Methods 0.000 claims description 7
- 229920003023 plastic Polymers 0.000 claims description 5
- 239000004033 plastic Substances 0.000 claims description 5
- 229910000838 Al alloy Inorganic materials 0.000 claims description 4
- 238000002347 injection Methods 0.000 claims description 4
- 239000007924 injection Substances 0.000 claims description 4
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 238000005507 spraying Methods 0.000 claims description 2
- 230000035882 stress Effects 0.000 claims 3
- 230000032683 aging Effects 0.000 claims 2
- 239000011701 zinc Substances 0.000 description 15
- 239000011777 magnesium Substances 0.000 description 14
- 239000010949 copper Substances 0.000 description 13
- 239000000203 mixture Substances 0.000 description 13
- 239000010936 titanium Substances 0.000 description 13
- 229910052725 zinc Inorganic materials 0.000 description 10
- 238000010791 quenching Methods 0.000 description 8
- 230000000171 quenching effect Effects 0.000 description 7
- 230000003068 static effect Effects 0.000 description 5
- 230000035945 sensitivity Effects 0.000 description 4
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 3
- 238000003754 machining Methods 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000004090 dissolution Methods 0.000 description 2
- 238000007654 immersion Methods 0.000 description 2
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 230000003042 antagnostic effect Effects 0.000 description 1
- 230000033228 biological regulation Effects 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 230000000694 effects Effects 0.000 description 1
- 238000005242 forging Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000000265 homogenisation Methods 0.000 description 1
- 239000000463 material Substances 0.000 description 1
- 238000011089 mechanical engineering Methods 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000005096 rolling process Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
Images
Classifications
-
- 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
- C22F1/053—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 zinc 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
-
- 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
- C22C21/10—Alloys based on aluminium with zinc as the next major constituent
Definitions
- the present invention generally relates to aluminum alloy products and, more particularly, to such thick 7xxx alloy products, their methods of manufacture and use.
- Thick aluminum blocks are also useful in the field of mechanical engineering.
- notch resistance is an important property of use for these products and it can be characterized for example by the NSR, which is the ratio between the elastic limit and the mechanical strength in the presence of a notch (" Sharp-Notch Strength-to-Yield Strength Ratio ") measured according to ASTM-E602.
- NSR the ratio between the elastic limit and the mechanical strength in the presence of a notch
- Sharp-Notch Strength-to-Yield Strength Ratio the ratio between the elastic limit and the mechanical strength in the presence of a notch
- a product is said to be quench sensitive if its static mechanical characteristics, such as its yield strength, decrease as the quenching rate decreases.
- the quenching rate is the average cooling rate of the product during quenching.
- the thick blocks should also preferably have low residual stresses. Indeed, the residual stresses cause deformations during the machining which affect the geometry of the mold.
- the residual stresses can be measured for example by the method described in the patent application WO 2004/053180 .
- low residual stresses we typically mean a W Tbar value of less than 4 kJ / m 3 , and in general of the order of 2 kJ / m 3
- the thick blocks must be obtained with a process as fast and economical as possible.
- the patent EP1587965 discloses an alloy useful for the manufacture of thick blocks, composition (in% by weight) 4.6-5.2% Zn; 2.6-3.0% Mg; 0.1-0.2% Cu; 0.05-0.2% Zr; not more than 0.05% Mn; not more than 0.05% Cr; not more than 0.15% Fe; not more than 0.15% Si; not more than 0.10% Ti and a method of manufacturing these blocks, in which the ingot obtained by continuous casting is used directly as a block.
- VMRBA The patent application FR 2,341,661 (VMRBA) describes a composition alloy (in% by weight) 4.0-6.2% Zn, 0.8-3.0% Mg, 0-1.5% Cu, 0.05 - 0.30% Zr, 0 - 0.20% Fe, 0-0.15% Si, 0-0.25% Mn, 0-0.10% Ti intended to be forged or kneaded by hot deformation and to be used for construction vehicles, machinery, equipment tanks and tools.
- the patent application JP81144031 discloses an alloy composition (in% by weight) 4.0-6.5% Zn, 0.4-1.8% Mg, 0.1-0.5% Cu, 0.1-0.5% Zr, and additionally 0.05-0.20% Mn and / or 0.05-0.20% Cr, for the production of tubes.
- the problem solved by the present invention is to obtain thick aluminum blocks having an improved property compromise between the static mechanical characteristics and the notch resistance, having a low level of residual stresses, by a rapid process. and economic.
- Yet another object of the invention is the use of a thick block according to the invention for the manufacture of mold for injection of plastics.
- Figure 1 Compromise obtained between the elastic limit R P.0,2 and the parameter called NSR ("Sharp-Notch Strength-to-Yield Strength Ratio"), which is the ratio of the notched specimen mechanical strength and the elastic limit R P0,2 .
- NSR Sharpp-Notch Strength-to-Yield Strength Ratio
- the static mechanical characteristics in other words the ultimate ultimate tensile strength R m , the tensile yield strength R p0,2 and the elongation at break A, are determined by a tensile test. according to standard EN 10002-1 or NF EN ISO 6892-1, the location to which the parts are taken and their meaning being defined by the EN 485-1 standard.
- the notched specimen mechanical strength is obtained in accordance with ASTM E602-03.
- the so-called NSR ratio between notched specimen strength and yield strength R P0.2 (“Sharp-Notch Strength-to-Yield Strength Ratio" is calculated. report gives an indication of the notch resistance of the sample.
- the problem is solved by an alloy comprising (in% by weight); Zn : 5.4 - 5.8 % , mg : 0.8 - 1.8 % Cu : ⁇ 0.2 % , Zr : 0.05 - 0.08 % , Ti ⁇ 0.15 % , mn ⁇ 0.1 % , Cr ⁇ 0.1 % , Yes ⁇ 0.15 % , Fe ⁇ 0.20 % , impurities with an individual content ⁇ 0.05% each and ⁇ 0.15% in total, remains aluminum.
- the combination of the zinc content of 5.4 - 5.8% by weight, the magnesium content of 0.8 to 1.8% and the copper content of less than 0.2% by weight makes it possible to achieve an improved compromise between mechanical strength and notch resistance.
- the preferred magnesium content is 1.0 to 1.4% by weight or even 1.1 to 1.3% by weight.
- the preferred copper content is less than 0.05% by weight or even less than 0.04% by weight.
- the zirconium content is 0.05 to 0.08% by weight, so as to further reduce the quenching sensitivity of the thick aluminum blocks.
- the titanium content is less than 0.15% by weight.
- an amount of titanium of between 0.01 and 0.05% by weight and preferably between 0.02 and 0.04% by weight is added in order to refine the grain size during casting.
- the Cr content and the Mn content are less than 0.1%.
- the Cr content is less than 0.05% by weight or even less than 0.03% by weight, and / or the Mn content is less than 0.05% by weight or even less than 0, 03% by weight, which allows in particular to further reduce the sensitivity to quenching thick aluminum blocks.
- Si and Fe are unavoidable impurities whose content is to be minimized so as in particular to improve the mechanical strength on the notched specimen.
- the Fe content is less than 0.20% by weight and preferably less than 0.15% by weight.
- the Si content is less than 0.15% by weight and preferably less than 0.10% by weight.
- the casting of the thick block is preferably carried out by semi-continuous casting with direct cooling ("Direct Chill Casting").
- the thick block has a thickness greater than 350 mm, and preferably greater than 450 mm or even greater than 550 mm.
- the block is essentially parallelepipedal in shape, it generally has a larger dimension (length), a second larger dimension (width) and a smaller dimension (thickness).
- the block may optionally then be homogenized, typically by a heat treatment at a temperature between 450 and 550 ° C for a period of 10 minutes to 30 hours and / or undergo a flash treatment at a temperature between 300 and 400 ° C for a period of 10 minutes to 30 hours followed by cooling to a temperature below 100 ° C.
- the block is then put into solution, that is to say heat-treated so that the block temperature reaches 500 to 560 ° C for a period of between 10 minutes and 5 hours, or even 20 hours.
- This heat treatment can be carried out at a constant temperature or in several stages.
- the block After dissolution, the block is cooled to a temperature below 100 ° C, preferably to room temperature.
- the cooling rate is at least 800 ° C / h.
- Such a cooling rate can be obtained by spraying or immersion in water. Since a cooling rate that is too high can generate excessive residual stresses in the blocks, water is preferably used at a temperature of at least 50.degree. C. and preferably at least 70.degree. C. for cooling.
- the block thus hardened is stripped, preferably by cold compression with a permanent deformation rate of between 1% and 5% and preferably between 2 and 4%. The stress relieving allows to reduce the residual stresses in the metal and to avoid the deformations during the machining.
- the income is made so that the block reaches a temperature of 120 and 170 ° C and preferably between 130 and 160 ° C for a period of 4 to 48 hours and preferably between 8 and 24 hours.
- an income is achieved to reach the T6 or T652 state, corresponding to the peak of the static mechanical properties (Rm and Rp0,2).
- said block does not undergo between the casting and the significant deformation step income by wrought.
- wrought is typically meant rolling operations or hot forging.
- significant deformation is meant that none of the dimensions of the cast block - which is a thick block of substantially parallelepiped shape (length L, width TL, thickness TC) - undergoes significant modification, that is to say typically at least about 10%, by heat treatment between casting and income.
- the thick blocks obtained by the process according to the invention have a compromise of advantageous properties, in particular between the elastic limit and the notch resistance, which are two antagonistic properties (the more important one is, the more other is weak). More specifically, the Applicant has found that for a thick block of an alloy having the composition according to the invention and having been obtained by following the claimed process steps until the income (casting, homogenization and stress relief optional, dissolution and quenching without significant wrought between the casting and the final step of income), regardless of the income treatment (mono- or multi-level) subsequently carried out to reach a given elastic limit Rp0.2, the NSR (“Sharp-Notch Strength-to-Yield Strength Ratio") parameter used to characterize the notch resistance of the block thus obtained, reaches a value that does not depend on the income treatment performed to obtain the targeted Rp02. For such thick blocks, a relationship between the RpO 2 and the NSR measured for example at 1 ⁇ 4 of the thickness can therefore be established, and this relationship appears to be substantially linear.
- the NSR
- the Applicant has been able to establish that the notch resistance, as evaluated at 1 ⁇ 4 thickness in the TL direction by the NSR (measured according to ASTM E602-03, paragraph 9.2) is greater than: - 0,017 * R p 0.2 + 6.7.
- the NSR is at least 0.8, preferably 1.0, and the yield strength is at least 320 MPa and preferably 330 MPa.
- Table 1 Chemical composition (% by weight) ⁇ / u> Reference Yes Fe Cu mn mg Zn Zr Cr Ti AT 0.05 0.08 0.02 0.01 1.2 5.7 0.08 ⁇ 0.01 0.04 B 0.05 0.08 0.03 ⁇ 0.01 1.2 5.6 0.08 ⁇ 0.01 0.04 VS 0.05 0.13 0.2 0.01 2.8 4.9 0.09 ⁇ 0.01 0.03 D 0.08 0.04 0.6 ⁇ 0.01 2.2 6.3 0.10 ⁇ 0.01 0.03
- Alloys A, B, C and D were cast as blocks of thickness 625 mm.
- the blocks of alloys A and C were transformed as follows: the blocks were first homogenized at 10h 480 ° C. The blocks were then dissolved for 4 hours at 540 ° C. and air-cooled at approximately 40 ° C./h (from 540 ° C. to 410 ° C. in 2 hours and then from 410 ° C. to 90 ° C. in 9 hours). ). The blocks were then first treated at 105 ° C for about 12 hours and then at 160 ° C for about 16 hours.
- the alloy blocks B and D were transformed as follows: the blocks first underwent a 2 hour expansion at 350 ° C. After being dissolved for 4 hours at 540 ° C. (Block B) or 10 hours at 475 ° C. (Block D), the blocks were cooled with water at 80 ° C. by immersion. The blocks then underwent compression straightening of 3%. The alloy blocks B were then tempered at 130 ° C for 24 h (block B1) or 150 ° C for 16 h (block B2). The alloy block D was first treated at 90 ° C for 8 to 12 hours and then at 160 ° C for 14 to 16 hours.
- the Figure 1 presents the compromise obtained between the elastic limit R P0,2 and the report called “Sharp-Notch Strength-to-Yield Strength Ratio", known under the abbreviation "NSR" and commonly used to characterize the sensitivity to the effect notch of a material.
- NSR Storage-Notch Strength-to-Yield Strength Ratio
- this parameter is the ratio between the mechanical strength measured on notched specimen and the elastic limit measured on non-notched specimen.
- ASTM E602-03 particularly in section 9.2.
- the alloy A allows, with respect to the alloy C, a simultaneous improvement in the yield strength and in the NSR ratio, and thus in the notch strength.
- the NSR report obtained is greater than -0.017 R p0.2 + 6.4.
- the process for converting the alloy according to the invention makes it possible to further improve the NSR ratio.
- the alloy block B according to the invention has an NSR ratio greater than -0.017 * R p0.2 + 6.7.
Description
La présente invention concerne en général des produits en alliage d'aluminium et, plus particulièrement, de tels produits épais en alliage 7xxx, leurs procédés de fabrication et d'utilisation.The present invention generally relates to aluminum alloy products and, more particularly, to such thick 7xxx alloy products, their methods of manufacture and use.
Dans le domaine des matières plastiques obtenues par injection, il existe une demande croissante pour des produits de grande dimension. De façon à réaliser les moules permettant de fabriquer ces produits de grande dimension, il est nécessaire d'utiliser des blocs épais, c'est-à-dire dont l'épaisseur est supérieure à 350 mm, et de préférence supérieure à 450 mm ou même supérieure à 550 mm. Par bloc, on entend un produit massif, de forme essentiellement parallélépipédique.In the field of plastics obtained by injection, there is a growing demand for large products. In order to produce the molds making it possible to manufacture these large products, it is necessary to use thick blocks, that is to say ones whose thickness is greater than 350 mm, and preferably greater than 450 mm or even greater than 550 mm. By block, we mean a massive product, essentially parallelepiped shape.
Les blocs épais en aluminium sont également utiles dans le domaine de l'ingénierie mécanique.Thick aluminum blocks are also useful in the field of mechanical engineering.
Les caractéristiques recherchées pour les blocs épais en aluminium destinés à la fabrication de moules sont des caractéristiques mécaniques statiques, telles que la limite d'élasticité ou la résistance à rupture, élevées ainsi qu'une bonne résistance à l'entaille, ces propriétés étant en général antinomiques. Ainsi la résistance à l'entaille est une propriété d'usage importante pour ces produits et elle peut être caractérisée par exemple par le NSR, qui est le rapport entre la limite d'élasticité et la résistance mécanique en présence d'une entaille (« Sharp-Notch Strength-to-Yield Strength Ratio ») mesuré selon la norme ASTM-E602. Pour les produits épais, ces propriétés doivent en particulier être obtenues à quart et/ou à mi-épaisseur et les produits doivent donc avoir une faible sensibilité à la trempe. On dit qu'un produit est sensible à la trempe si ses caractéristiques mécaniques statiques, telles que sa limite élastique, décroissent lorsque la vitesse de trempe décroît. La vitesse de trempe est la vitesse de refroidissement moyenne du produit au cours de la trempe.The characteristics required for the thick aluminum blocks for the manufacture of molds are static mechanical characteristics, such as the yield strength or the breaking strength, high as well as a good notch resistance, these properties being in good condition. general antinomies. Thus notch resistance is an important property of use for these products and it can be characterized for example by the NSR, which is the ratio between the elastic limit and the mechanical strength in the presence of a notch (" Sharp-Notch Strength-to-Yield Strength Ratio ") measured according to ASTM-E602. For thick products, these properties must in particular be obtained at quarter and / or at mid-thickness and the products must therefore have a low sensitivity to quenching. A product is said to be quench sensitive if its static mechanical characteristics, such as its yield strength, decrease as the quenching rate decreases. The quenching rate is the average cooling rate of the product during quenching.
Les blocs épais doivent aussi de préférence avoir de faibles contraintes résiduelles. En effet, les contraintes résiduelles provoquent des déformations lors de l'usinage qui affectent la géométrie du moule. Les contraintes résiduelles peuvent être mesurées par exemple par la méthode décrite dans la demande de brevet
Enfin, les blocs épais doivent être obtenus avec un procédé aussi rapide et économique que possible.Finally, the thick blocks must be obtained with a process as fast and economical as possible.
Le brevet
La demande internationale
Des alliages de composition voisine sont également connus pour d'autres applications. Sont par exemple enregistrés auprès de l'Aluminium Association:
- l'alliage 7003 qui a la composition suivante:
5,0 % - 6,5 % Zn; 0,50-1,0 % Mg; 0.05-0,25 % Zr; 0-0,20 % Cu; 0-0,35 % Fe; 0-0,30 % Si; 0-0,30% Mn; 0-0,20% Cr; 0-0,20 % Ti; balance Al avec impuretés inévitables <0,05 %, total <0,15% - l'alliage 7021 qui a la composition suivante:
5,0 % - 6,0 % Zn; 1,2-1,8 % Mg; 0.08-0,18 % Zr; 0-0,25 % Cu; 0-0,40 % Fe; 0-0,25 % Si; 0-0,10% Mn; 0-0,05% Cr; 0-0,10 % Ti; balance Al avec impuretés inévitables <0,05 %, total <0,15%
- the alloy 7003 which has the following composition:
5.0% - 6.5% Zn; 0.50-1.0% Mg; 0.05-0.25% Zr; 0-0.20% Cu; 0-0.35% Fe; 0-0.30% Si; 0-0.30% Mn; 0-0.20% Cr; 0-0.20% Ti; Al balance with unavoidable impurities <0.05%, total <0.15% - alloy 7021 which has the following composition:
5.0% - 6.0% Zn; 1.2-1.8% Mg; 0.08-0.18% Zr; 0-0.25% Cu; 0-0.40% Fe; 0-0.25% Si; 0-0.10% Mn; 0-0.05% Cr; 0-0.10% Ti; Al balance with unavoidable impurities <0.05%, total <0.15%
Le brevet
La demande de brevet
La demande de brevet
Le problème que cherche à résoudre la présente invention est d'obtenir des blocs d'aluminium épais présentant un compromis de propriétés amélioré entre les caractéristiques mécaniques statiques et la résistance à l'entaille, ayant un faible niveau de contraintes résiduelles, par un procédé rapide et économique.The problem solved by the present invention is to obtain thick aluminum blocks having an improved property compromise between the static mechanical characteristics and the notch resistance, having a low level of residual stresses, by a rapid process. and economic.
L'objet de l'invention est un procédé de fabrication d'un bloc d'aluminium dont l'épaisseur est supérieure à 350 mm comprenant les étapes de : (a) coulée d'un bloc épais en alliage d'aluminium comprenant (en % en poids): Zn: 5,4-5,8%, Mg: 0,8 - 1,8 %, Cu : < 0,2 %, Zr: 0,05 - 0,08 %, Ti: < 0,15 %, Mn: < 0,1 %, Cr: < 0,1 %, Si: < 0,15 %, Fe: < 0,20 %, impuretés ayant une teneur individuelle < 0,05 % chacune et < 0,15% au total, reste aluminium;
- (b) optionnellement, homogénéisation à une température comprise entre 450 et 550 °C pendant une durée de 10 minutes à 30 heures et/ou détente à une température comprise entre 300 et 400 °C pendant une durée de 10 minutes à 30 heures suivi d'un refroidissement jusqu'à une température inférieure à 100 °C;
- (c) mise en solution dudit bloc coulé à une température de 500 à 560°C pendant 10 mn à 20 heures,
- (d) refroidissement dudit bloc mis en solution jusqu'à une température inférieure à 100 °C réalisé avec une vitesse de refroidissement au moins égale à 800 °C/h puis détensionnement du bloc ainsi mis en solution et refroidi par une compression contrôlée avec une déformation permanente comprise entre 1% et 5%;
- (e) revenu dudit bloc mis en solution et refroidi, par chauffage à 120 à 170°C pendant 4 à 48 heures,
- (b) optionally, homogenizing at a temperature between 450 and 550 ° C for a period of 10 minutes to 30 hours and / or expansion at a temperature between 300 and 400 ° C for a period of 10 minutes to 30 hours followed by cooling to a temperature below 100 ° C;
- (c) dissolving said cast block at a temperature of 500 to 560 ° C for 10 minutes to 20 hours,
- (d) cooling said block in solution to a temperature below 100 ° C achieved with a cooling rate of at least 800 ° C / h and then stress relieving the block so dissolved and cooled by a controlled compression with a permanent deformation of between 1% and 5%;
- (e) returning said block dissolved and cooled, by heating at 120 to 170 ° C for 4 to 48 hours,
Un autre objet de l'invention est un bloc épais d'aluminium susceptible d'être obtenu par le procédé selon l'invention caractérisé en ce que, à ¼ épaisseur dans la direction TL, la limite d'élasticité RP0,2 et le rapport appelé NSR entre la résistance mécanique sur éprouvette entaillée et la limite d'élasticité RP0,2 mesuré selon la norme ASTM E602-03, paragraphe 9.2 sont tels que:
- Rp0,2 > 320 MPa, de
préférence 330 MPa
et/ou - NSR > 0,8, de préférence 1,0.
- R p0.2 > 320 MPa, preferably 330 MPa
and or - NSR> 0.8, preferably 1.0.
Encore un autre objet de l'invention est l'utilisation d'un bloc épais selon l'invention pour la fabrication de moule pour injection des plastiques.Yet another object of the invention is the use of a thick block according to the invention for the manufacture of mold for injection of plastics.
Sauf mention contraire, toutes les indications concernant la composition chimique des alliages sont exprimées comme un pourcentage en poids basé sur le poids total de l'alliage. La désignation des alliages se fait en conformité avec les règlements de The Aluminium Association, connus de l'homme du métier. Les définitions des états métallurgiques sont indiquées dans la norme européenne EN 515.Unless stated otherwise, all the information concerning the chemical composition of the alloys is expressed as a percentage by weight based on the total weight of the alloy. The designation of alloys is in accordance with the regulations of The Aluminum Association, known to those skilled in the art. The definitions of the metallurgical states are given in the European standard EN 515.
Sauf mention contraire, les caractéristiques mécaniques statiques, en d'autres termes la résistance à la rupture ultime Rm, la limite d'élasticité en traction Rp0,2 et l'allongement à la rupture A, sont déterminées par un essai de traction selon la norme EN 10002-1 ou NF EN ISO 6892-1, l'emplacement auquel les pièces sont prises et leur sens étant définis par la norme EN 485-1. La résistance mécanique sur éprouvette entaillée est obtenue conformément à la norme ASTM E602-03. Conformément à la norme E602-03, paragraphe 9.2, on calcule le rapport appelé NSR entre la résistance mécanique sur éprouvette entaillée et la limite d'élasticité RP0,2 (« Sharp-Notch Strength-to-Yield Strength Ratio »), ce rapport donne une indication de la résistance à l'entaille de l'échantillon.Unless otherwise stated, the static mechanical characteristics, in other words the ultimate ultimate tensile strength R m , the tensile yield strength R p0,2 and the elongation at break A, are determined by a tensile test. according to standard EN 10002-1 or NF EN ISO 6892-1, the location to which the parts are taken and their meaning being defined by the EN 485-1 standard. The notched specimen mechanical strength is obtained in accordance with ASTM E602-03. In accordance with E602-03, paragraph 9.2, the so-called NSR ratio between notched specimen strength and yield strength R P0.2 ("Sharp-Notch Strength-to-Yield Strength Ratio") is calculated. report gives an indication of the notch resistance of the sample.
Le problème posé est résolu grâce à un alliage comprenant (en % en poids) ;
La combinaison de la teneur en zinc de 5,4 - 5,8% en poids, de la teneur en magnésium de 0,8 à 1,8 % et de la teneur en cuivre inférieure à 0,2% en poids permet d'atteindre un compromis amélioré entre la résistance mécanique et la résistance à l'entaille. La teneur préféré en magnésium est de 1,0 à 1,4 % en poids ou même de 1,1 à 1,3 % en poids. La teneur préférée en cuivre est inférieure à 0,05 % en poids ou même inférieure à 0,04 % en poids.The combination of the zinc content of 5.4 - 5.8% by weight, the magnesium content of 0.8 to 1.8% and the copper content of less than 0.2% by weight makes it possible to achieve an improved compromise between mechanical strength and notch resistance. The preferred magnesium content is 1.0 to 1.4% by weight or even 1.1 to 1.3% by weight. The preferred copper content is less than 0.05% by weight or even less than 0.04% by weight.
La teneur en zirconium est de 0,05 à 0,08% en poids, de façon notamment à diminuer encore la sensibilité à la trempe des blocs épais en aluminium.The zirconium content is 0.05 to 0.08% by weight, so as to further reduce the quenching sensitivity of the thick aluminum blocks.
La teneur en titane est inférieure à 0,15 % en poids. De façon avantageuse, une quantité de titane comprise entre 0,01 et 0,05% en poids et préférentiellement comprise entre 0,02 et 0,04% en poids est ajoutée de façon à affiner la taille de grain lors de la coulée.The titanium content is less than 0.15% by weight. Advantageously, an amount of titanium of between 0.01 and 0.05% by weight and preferably between 0.02 and 0.04% by weight is added in order to refine the grain size during casting.
La teneur en Cr et la teneur en Mn sont inférieures à 0,1%. De manière préférée, la teneur en Cr est inférieure à 0,05% en poids ou même inférieure à 0,03% en poids, et/ou la teneur en Mn est inférieure à 0,05% en poids ou même inférieure à 0,03% en poids, ce qui permet en particulier de diminuer encore la sensibilité à la trempe des blocs épais en aluminium.The Cr content and the Mn content are less than 0.1%. Preferably, the Cr content is less than 0.05% by weight or even less than 0.03% by weight, and / or the Mn content is less than 0.05% by weight or even less than 0, 03% by weight, which allows in particular to further reduce the sensitivity to quenching thick aluminum blocks.
Si et Fe sont des impuretés inévitables dont on cherche à minimiser la teneur de façon en particulier à améliorer la résistance mécanique sur éprouvette entaillée. La teneur en Fe est inférieure à 0,20 % en poids et de manière préférée inférieure à 0,15 % en poids. La teneur en Si est inférieure à 0,15 % en poids et de manière préférée inférieure à 0,10 % en poids.Si and Fe are unavoidable impurities whose content is to be minimized so as in particular to improve the mechanical strength on the notched specimen. The Fe content is less than 0.20% by weight and preferably less than 0.15% by weight. The Si content is less than 0.15% by weight and preferably less than 0.10% by weight.
Un procédé approprié pour fabriquer des blocs épais en alliage selon l'invention comprend les étapes de
- (a) coulée d'un bloc épais en alliage d'aluminium comprenant (en % en poids) :Zn: 5,4-5,8%,Mg: 0,8 - 1,8 %,Cu : < 0,2 %,Zr : 0,05 - 0,08 %,Ti: < 0,15 %,Mn: < 0,1 %,Cr: < 0,1 %,Si: < 0,15 %,Fe: < 0,20 %, impuretés ayant une teneur individuelle < 0,05 % chacune et < 0,15% au total, reste aluminium ;
- (b) optionnellement, homogénéisation à une température comprise entre 450 et 550 °C pendant une durée de 10 minutes à 30 heures et/ou détente à une température comprise entre 300 et 400 °C pendant une durée de 10 minutes à 30 heures suivi d'un refroidissement jusqu'à une température inférieure à 100 °C;
- (c) mise en solution dudit bloc coulé à une température de 500 à 560°C pendant 10 mn à 20 heures,
- (d) refroidissement dudit bloc mis en solution jusqu'à une température inférieure à 100 °C, réalisé avec une vitesse de refroidissement au moins égale à 800 °C/h puis détensionnement du bloc ainsi mis en solution et refroidi par une compression contrôlée avec une déformation permanente comprise entre 1% et 5%;
- (e) revenu dudit bloc mis en solution et refroidi, par chauffage à 120 à 170°C pendant 4 à 48 heures, dans lequel aucune des dimensions dudit bloc coulé ne subit de déformation d'au moins 10% par corroyage entre les étapes de coulée et de revenu.
- (a) casting of a thick block of aluminum alloy comprising (in% by weight): Zn: 5.4-5.8%, Mg: 0.8 - 1.8%, Cu: <0.2 %, Zr: 0.05 - 0.08%, Ti: <0.15%, Mn: <0.1%, Cr: <0.1%, Si: <0.15%, Fe: <0, 20%, impurities with an individual content <0.05% each and <0.15% in total, remains aluminum;
- (b) optionally, homogenizing at a temperature between 450 and 550 ° C for a period of 10 minutes to 30 hours and / or expansion at a temperature between 300 and 400 ° C for a period of 10 minutes to 30 hours followed by cooling to a temperature below 100 ° C;
- (c) dissolving said cast block at a temperature of 500 to 560 ° C for 10 minutes to 20 hours,
- (d) cooling said block dissolved in a temperature of less than 100 ° C., carried out with a cooling rate of at least 800 ° C./h, and then relieving the block thus put into solution and cooled by a controlled compression with permanent deformation of between 1% and 5%;
- (e) returning said block dissolved and cooled, by heating at 120 to 170 ° C for 4 to 48 hours, wherein none of the dimensions of said cast block undergoes deformation of at least 10% by wrought between the steps of casting and income.
La coulée du bloc épais est de préférence réalisée par coulée semi-continue avec refroidissement direct (« Direct Chill casting »). Le bloc épais a une épaisseur supérieure à 350 mm, et de préférence supérieure à 450 mm ou même supérieure à 550 mm. Le bloc est de forme essentiellement parallélépipédique, il a en général une plus grande dimension (longueur), une seconde plus grande dimension (largeur) et une plus petite dimension (épaisseur).The casting of the thick block is preferably carried out by semi-continuous casting with direct cooling ("Direct Chill Casting"). The thick block has a thickness greater than 350 mm, and preferably greater than 450 mm or even greater than 550 mm. The block is essentially parallelepipedal in shape, it generally has a larger dimension (length), a second larger dimension (width) and a smaller dimension (thickness).
Le bloc peut optionnellement être ensuite homogénéisé, typiquement par un traitement thermique à une température comprise entre 450 et 550 °C pendant une durée de 10 minutes à 30 heures et/ou subir un traitement de détente à une température comprise entre 300 et 400 °C pendant une durée de 10 minutes à 30 heures suivi d'un refroidissement jusqu'à une température inférieure à 100 °C.The block may optionally then be homogenized, typically by a heat treatment at a temperature between 450 and 550 ° C for a period of 10 minutes to 30 hours and / or undergo a flash treatment at a temperature between 300 and 400 ° C for a period of 10 minutes to 30 hours followed by cooling to a temperature below 100 ° C.
Le bloc est ensuite mis en solution c'est-à-dire traité thermiquement de façon à ce que la température du bloc atteigne 500 à 560°C pendant une durée comprise entre 10 mn et 5 heures, voire 20 heures. Ce traitement thermique peut être réalisé à température constante ou en plusieurs paliers.The block is then put into solution, that is to say heat-treated so that the block temperature reaches 500 to 560 ° C for a period of between 10 minutes and 5 hours, or even 20 hours. This heat treatment can be carried out at a constant temperature or in several stages.
Après mise en solution, le bloc est refroidi jusqu'à une température inférieure à 100 °C, de préférence jusqu'à température ambiante. La vitesse de refroidissement est au moins égale à 800 °C/h. Une telle vitesse de refroidissement peut être obtenue par aspersion ou immersion à l'eau. Une vitesse de refroidissement trop élevée pouvant générer des contraintes résiduelles trop importantes dans les blocs, on utilise de préférence de l'eau à une température d'au moins 50 °C et de préférence d'au moins 70 °C pour le refroidissement. Dans ce second mode de réalisation on détensionne le bloc ainsi trempé, de préférence par compression à froid avec un taux de déformation permanente compris entre 1 % et 5 % et de préférence compris entre 2 et 4%. Le détensionnement permet de diminuer les contraintes résiduelles dans le métal et d'éviter les déformations lors de l'usinage.After dissolution, the block is cooled to a temperature below 100 ° C, preferably to room temperature. The cooling rate is at least 800 ° C / h. Such a cooling rate can be obtained by spraying or immersion in water. Since a cooling rate that is too high can generate excessive residual stresses in the blocks, water is preferably used at a temperature of at least 50.degree. C. and preferably at least 70.degree. C. for cooling. In this second embodiment, the block thus hardened is stripped, preferably by cold compression with a permanent deformation rate of between 1% and 5% and preferably between 2 and 4%. The stress relieving allows to reduce the residual stresses in the metal and to avoid the deformations during the machining.
Enfin, on réalise le revenu du bloc ainsi mis en solution et refroidi. Le revenu est réalisé de manière à ce que le bloc atteigne une température de 120 et 170 °C et de manière préférée entre 130 et 160 °C pendant une durée de 4 à 48 heures et de manière préférée entre 8 et 24 heures. Avantageusement, on réalise un revenu pour atteindre l'état T6 ou T652, correspondant au pic des propriétés mécaniques statiques (Rm et Rp0,2).Finally, one realizes the income of the block thus put in solution and cooled. The income is made so that the block reaches a temperature of 120 and 170 ° C and preferably between 130 and 160 ° C for a period of 4 to 48 hours and preferably between 8 and 24 hours. Advantageously, an income is achieved to reach the T6 or T652 state, corresponding to the peak of the static mechanical properties (Rm and Rp0,2).
Entre chaque opération, il est possible d'effectuer des opérations simples de sciage du bloc et/ou d'usinage des surfaces.Between each operation, it is possible to perform simple operations of sawing the block and / or machining surfaces.
Par contre, ledit bloc ne subit pas entre la coulée et le revenu d'étape de déformation significative par corroyage. Par "corroyage", on entend typiquement des opérations de laminage ou forgeage à chaud. Par "déformation significative", on entend qu'aucune des dimensions du bloc coulé - lequel est un bloc épais de forme essentiellement parallélépipédique (longueur L, largeur TL, épaisseur TC) - ne subit de modification significative, c'est-à-dire typiquement d'au moins environ 10%, par corroyage entre la coulée et le revenu. En d'autres termes, aucune des dimensions du bloc coulé ne subit par corroyage une variation relative typiquement supérieure à 10% en valeur absolue, ce qui signifie que ledit corroyage n'entraîne aucune déformation permanente dans chaque direction L, TL, TC supérieure à une valeur voisine de Ln(1,1)= 0,095 et correspond à une déformation plastique généralisée
Les blocs épais obtenus par le procédé selon l'invention présentent un compromis de propriétés avantageux, en particulier entre la limite élastique et la résistance à l'effet d'entaille qui sont deux propriétés antagonistes (plus l'une est importante, plus l'autre est faible). Plus précisément, la demanderesse a constaté que, pour un bloc épais en un alliage ayant la composition selon l'invention et ayant été obtenu en suivant les étapes revendiquées du procédé jusqu'au revenu (coulée, homogénéisation et détensionnement optionnels, mise en solution et trempe sans qu'il y ait corroyage significatif entre la coulée et l'étape finale de revenu), quel que soit le traitement de revenu (mono- ou multi-paliers) réalisé ensuite pour atteindre une limite élastique Rp0,2 donnée, le NSR (« Sharp-Notch Strength-to-Yield Strength Ratio »), paramètre utilisé pour caractériser la résistance à l'effet d'entaille du bloc ainsi obtenu, atteint une valeur qui ne dépend pas du traitement de revenu effectué pour obtenir le Rp02 visé. On peut par conséquent établir pour de tels blocs épais une relation entre le Rp02 et le NSR mesurés par exemple au ¼ de l'épaisseur, et cette relation apparaît sensiblement linéaire.The thick blocks obtained by the process according to the invention have a compromise of advantageous properties, in particular between the elastic limit and the notch resistance, which are two antagonistic properties (the more important one is, the more other is weak). More specifically, the Applicant has found that for a thick block of an alloy having the composition according to the invention and having been obtained by following the claimed process steps until the income (casting, homogenization and stress relief optional, dissolution and quenching without significant wrought between the casting and the final step of income), regardless of the income treatment (mono- or multi-level) subsequently carried out to reach a given elastic limit Rp0.2, the NSR ("Sharp-Notch Strength-to-Yield Strength Ratio") parameter used to characterize the notch resistance of the block thus obtained, reaches a value that does not depend on the income treatment performed to obtain the targeted Rp02. For such thick blocks, a relationship between the RpO 2 and the NSR measured for example at ¼ of the thickness can therefore be established, and this relationship appears to be substantially linear.
Ainsi, la demanderesse a pu établir que, la résistance à l'entaille, telle qu'évaluée à ¼ épaisseur dans la direction TL par le NSR (mesuré en suivant la norme ASTM E602-03, paragraphe 9.2) est supérieure à:
Typiquement, le NSR est d'au moins 0,8 , de préférence 1,0 et la limite d'élasticité est d'au moins 320 MPa et de préférence 330 MPa.Typically, the NSR is at least 0.8, preferably 1.0, and the yield strength is at least 320 MPa and preferably 330 MPa.
L'obtention simultanée d'une résistance mécanique élevée et d'une résistance à l'entaille élevée est un résultat surprenant.Obtaining both high mechanical strength and high notch resistance is a surprising result.
Les blocs épais selon l'invention sont utilisés de façon avantageuse pour la fabrication de moules pour injection des plastiquesThe thick blocks according to the invention are advantageously used for the manufacture of molds for injection of plastics
L'exemple de l'invention est référencé B. Les exemples A, C et D sont présentés à titre de comparaison. Les compositions chimiques des différents alliages testés dans cet exemple sont fournies dans le tableau 1.
Les alliages A, B, C et D ont été coulés sous forme de blocs d'épaisseur 625 mm.Alloys A, B, C and D were cast as blocks of thickness 625 mm.
Les blocs en alliages A et C ont été transformés de la façon suivante : les blocs ont d'abord été homogénéisés 10h 480°C. Les blocs ont ensuite été mis en solution 4h à 540 °C et refroidis à l'air à environ 40 °C/h (de 540 °C à 410 °C en 2 heures puis de 410 °C à 90 °C en 9 heures). Les blocs ont ensuite subi un traitement de revenu d'abord à 105 °C pendant environ 12 heures puis à 160 °C pendant environ 16 h.The blocks of alloys A and C were transformed as follows: the blocks were first homogenized at 10h 480 ° C. The blocks were then dissolved for 4 hours at 540 ° C. and air-cooled at approximately 40 ° C./h (from 540 ° C. to 410 ° C. in 2 hours and then from 410 ° C. to 90 ° C. in 9 hours). ). The blocks were then first treated at 105 ° C for about 12 hours and then at 160 ° C for about 16 hours.
Les blocs en alliages B et D ont été transformés de la façon suivante : les blocs ont d'abord subi une détente de 2 heures à 350 °C. Après mise en solution pendant 4 h à 540°C (bloc B) ou 10 h à 475°C (bloc D), les blocs ont été refroidis avec de l'eau à 80 °C par immersion. Les blocs ont ensuite subi un détensionnement par compression de 3%. Les blocs en alliage B ont ensuite subi un revenu de 130 °C pendant 24 h (bloc B1) ou de 150°C pendant 16 h (bloc B2). Le bloc en alliage D a quant à lui subi un traitement de revenu d'abord à 90°C pendant 8 à 12 h puis à 160°C pendant 14 à 16 h.The alloy blocks B and D were transformed as follows: the blocks first underwent a 2 hour expansion at 350 ° C. After being dissolved for 4 hours at 540 ° C. (Block B) or 10 hours at 475 ° C. (Block D), the blocks were cooled with water at 80 ° C. by immersion. The blocks then underwent compression straightening of 3%. The alloy blocks B were then tempered at 130 ° C for 24 h (block B1) or 150 ° C for 16 h (block B2). The alloy block D was first treated at 90 ° C for 8 to 12 hours and then at 160 ° C for 14 to 16 hours.
Les caractéristiques mécaniques obtenues, mesurées à ¼ épaisseur dans la direction TL sont présentées dans le tableau 2
La
Dans des conditions de transformations identiques, l'alliage A, permet par rapport à l'alliage C une amélioration simultanée de la limite d'élasticité et du rapport NSR, donc de la résistance à l'entaille. Le rapport NSR obtenu est supérieur à
-0,017 Rp0,2 + 6,4.Under identical transformation conditions, the alloy A allows, with respect to the alloy C, a simultaneous improvement in the yield strength and in the NSR ratio, and thus in the notch strength. The NSR report obtained is greater than
-0.017 R p0.2 + 6.4.
Le procédé de transformation de l'alliage selon l'invention permet d'améliorer encore le rapport NSR. Ainsi le bloc en alliage B selon l'invention atteint un rapport NSR supérieur à -0,017 * Rp0,2 + 6,7.The process for converting the alloy according to the invention makes it possible to further improve the NSR ratio. Thus, the alloy block B according to the invention has an NSR ratio greater than -0.017 * R p0.2 + 6.7.
Ce rapport n'est pas atteint par l'alliage D dans des conditions de transformation semblables.This ratio is not reached by alloy D under similar processing conditions.
Claims (6)
- Method for manufacturing an aluminium block wherein the thickness is greater than 350 mm comprising steps for:(a) casting a thick aluminium alloy block comprising (as a % by weight):
Zn: 5.4 - 5.8%, Mg: 0.8 - 1.8%, Cu: < 0.2%, Zr: 0.05 - 0.08%, Ti : < 0.15%, Mn : < 0.1%, Cr : < 0.1%, Si: < 0.15%, Fe : < 0.20%, (b) optionally, homogenising at a temperature between 450 and 550°C for a period of 10 minutes to 30 hours and/or stress relief at a temperature between 300 and 400°C for a period of 10 minutes to 30 hours followed by cooling to a temperature less than 100°C;(c) solution heat treatment of said cast block at a temperature of 500 to 560°C for 10 min to 20 hours,(d) cooling of said solution-heat treated block to a temperature less than 100°C, carried out with a cooling rate at least equal to 800°C/hour followed by stress relief of the solution-heat treated and cooled block by controlled compression with a permanent set between 1% and 5%(e) aging of said solution-heat treated and cooled block, by heating at 120 to 170°C for 4 to 48 hours,wherein none of the dimensions of said cast block is subject to strain of at least 10% by working between the casting and aging steps. - Method according to claim 1 wherein the solution-heat treated and cooled block undergoes stress relief with a permanent set between 2 and 4%.
- Method according to claim 2 wherein the cooling of step (d) is carried out by spraying with or immersing in water at a temperature of at least 50°C and preferably of at least 70°C.
- Aluminium block wherein the thickness is greater than 350 mm suitable for being obtained using the method according to any one of claims 1 to 3,
said block comprising (as a % by weight): Zn: 5.4 - 5.8%, Mg: 0.8 - 1.8%, Cu: < 0.2%, Zr: 0.05 - 0.08%, Ti: < 0.15%, Mn: < 0.1%, Cr: < 0.1%, Si: < 0.15%, Fe: < 0.20%, impurities having an individual content < 0.05% each and < 0.15% in total, remainder aluminium; and
characterised in that, at ¼ thickness in the direction TL, the yield strength RP0.2 expressed in MPa and the ratio referred to as NSR between the mechanical strength on a notched test piece and the yield strength RP0.2 measured as per the standard ASTM E602-03, paragraph 9.2 are such that:- NSR > -0.017 * Rp0.2 + 6.7 and- Rp0.2 > 320 M Pa, preferably 330 MPa. - Aluminium block according to claim 4 characterised in that NSR > 0.8, preferably 1.0.
- Use of a thick block according to any one of claims 4 to 5 for the manufacture of moulds for the injection of plastics.
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2010
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2011
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- 2011-12-06 JP JP2013543846A patent/JP6118728B2/en active Active
- 2011-12-06 CA CA2820768A patent/CA2820768A1/en not_active Abandoned
- 2011-12-06 PL PL11808242T patent/PL2652163T3/en unknown
- 2011-12-06 WO PCT/FR2011/000637 patent/WO2012080592A1/en active Application Filing
- 2011-12-06 EP EP11808242.9A patent/EP2652163B1/en active Active
- 2011-12-06 KR KR1020137017601A patent/KR101900973B1/en active IP Right Grant
- 2011-12-06 US US13/994,097 patent/US11306379B2/en active Active
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- 2022-02-23 US US17/678,591 patent/US20220389558A1/en active Pending
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WO2008003506A2 (en) * | 2006-07-07 | 2008-01-10 | Aleris Aluminum Koblenz Gmbh | Aa7000-series aluminium alloy products and a method of manufacturing thereof |
Cited By (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US10835942B2 (en) | 2016-08-26 | 2020-11-17 | Shape Corp. | Warm forming process and apparatus for transverse bending of an extruded aluminum beam to warm form a vehicle structural component |
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 |
Also Published As
Publication number | Publication date |
---|---|
PL2652163T3 (en) | 2019-05-31 |
MX354911B (en) | 2018-03-26 |
FR2968675A1 (en) | 2012-06-15 |
CL2013001716A1 (en) | 2013-12-06 |
US11306379B2 (en) | 2022-04-19 |
WO2012080592A1 (en) | 2012-06-21 |
KR20140012628A (en) | 2014-02-03 |
US20220389558A1 (en) | 2022-12-08 |
CA2820768A1 (en) | 2012-06-21 |
MX2013006848A (en) | 2013-11-01 |
US20130284322A1 (en) | 2013-10-31 |
JP2014505786A (en) | 2014-03-06 |
FR2968675B1 (en) | 2013-03-29 |
EP2652163A1 (en) | 2013-10-23 |
JP6118728B2 (en) | 2017-04-19 |
KR101900973B1 (en) | 2018-09-20 |
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