EP0645467A1 - Process for desensitization to intercristalline corrosion of alumium alloys of the series 2000 and 6000, and articles made according to this process - Google Patents
Process for desensitization to intercristalline corrosion of alumium alloys of the series 2000 and 6000, and articles made according to this process Download PDFInfo
- Publication number
- EP0645467A1 EP0645467A1 EP94420256A EP94420256A EP0645467A1 EP 0645467 A1 EP0645467 A1 EP 0645467A1 EP 94420256 A EP94420256 A EP 94420256A EP 94420256 A EP94420256 A EP 94420256A EP 0645467 A1 EP0645467 A1 EP 0645467A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloys
- series
- corrosion
- intercrystalline corrosion
- states
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Withdrawn
Links
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
-
- 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
-
- 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
- C22F1/057—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 copper as the next major constituent
Definitions
- the present invention relates to a method for desensitizing to intercrystalline corrosion (CI) of aluminum alloys belonging to the 2000 and 6000 series of the nomenclature of the Aluminum Association and the corresponding products.
- CI intercrystalline corrosion
- the 2000 (or 6000) alloys concerned contain respectively Cu or Cu + Mg (or Si + Mg or Si + Mg + Cu) as main elements, possible minor elements such as Mn , Cr, Zr, Zn, Ag and unavoidable processing impurities such as Fe up to 1% and Si up to 1% (in 2000 alloys only in the latter case), other elements, including Li, with a maximum content of 0.05% each and 0.15% in total. (Unless otherwise indicated, the compositions refer to the weight content).
- the alloys concerned are dissolved, quenched, possibly hardened by controlled deformation and cured and / or tempered. In this state, these alloys are sensitive to intercrystalline corrosion, which limits their use in aggressive conditions, in particular in a marine atmosphere for long exposures.
- the method according to the invention consists, in the range of heat treatment of these alloys, in practicing a solution in a temperature range located from 10 to 100 ° C below the conventional solution temperature (Tms) .
- this temperature range is preferably kept from 10 to 30 ° C below Tms.
- alloys 6013 or 6056, used in T6, T6xx or under-income states or delivered in T3xx or T4 states it is required from 10 to 100 ° C below Tms.
- the Tms solution temperature is known to those skilled in the art.
- this dissolution temperature generally corresponds to obtaining a solid solution most saturated with hardening elements, compatible with the chemical composition of the alloy considered and the practical constraints of industrial heat treatments.
- the applicant company noted that the products desensitized to IC could be characterized by two physical parameters, taken individually or in combination. This is the conductivity electrical surface and AED signal.
- the surface electrical conductivity of the alloys according to the invention is at least 0.7 MS / m higher than that of the alloys according to the prior art treated under analogous conditions, except as regards the solution temperature.
- the energy associated with the AED peak relating to the fusion of the eutectics of the alloys according to the invention, determined under the conditions reported below, is at least 3 J / g (in absolute value) greater than that relating to the corresponding peak classic alloys.
- the AED thermograms are plotted at a heating rate of 20 ° C / min on samples of approximately 50 mg (PERKIN ELMER DSC7 device).
- the first temperature (495 ° C) corresponds to the "classic" solution of the alloy.
- a 2000 x 1000 mm sheet of alloy 6013 with a composition by weight: 0.82% Si; 0.22% Fe; 0.92% Cu; 0.9% Mg; 0.62% Mn; 0.15% Zn; ⁇ 0.08% Ti and 6 mm thick was dissolved under the conditions reported in Table II, operation followed by quenching in cold water, two days maturation and tempering of the type T6 (6 hours at 175 ° C).
- a comparison is made with a conventional solution treatment (30 minutes at 550 ° C.), followed by quenching in cold water, two days maturation and an income of the T6 type (6 hours at 175 ° C).
- alloys treated according to the invention have a resistance to intercrystalline corrosion substantially improved compared to that of those obtained according to the prior art.
- the alloys obtained according to the invention can be used in particular in the field of mechanical engineering and transport industries (rail, automobile, aeronautics, maritime).
Landscapes
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Preventing Corrosion Or Incrustation Of Metals (AREA)
- Prevention Of Electric Corrosion (AREA)
- Electroplating Methods And Accessories (AREA)
Abstract
Description
La présente invention concerne un procédé de désensibilisation à la corrosion intercristalline (CI) des alliages d'Aluminium appartenant aux séries 2000 et 6000 de la nomenclature de l'Aluminum Association et les produits correspondants.The present invention relates to a method for desensitizing to intercrystalline corrosion (CI) of aluminum alloys belonging to the 2000 and 6000 series of the nomenclature of the Aluminum Association and the corresponding products.
Dans le cadre de cette demande de brevet, les alliages 2000 (ou 6000) concernés contiennent respectivement du Cu ou du Cu+Mg (ou du Si+Mg ou Si+Mg+Cu) comme éléments principaux, des éléments mineurs éventuels tel que Mn,Cr,Zr, Zn, Ag et les impuretés inévitables d'élaboration telles que le Fe jusqu'à 1% et le Si jusqu'à 1% (dans les alliages 2000 seulement dans ce dernier cas), les autres éléments, y compris le Li, ayant une teneur maximale de 0,05% chacun et 0,15% au total. (Sauf indication contraire, les compositions se réfèrent à la teneur pondérale).In the context of this patent application, the 2000 (or 6000) alloys concerned contain respectively Cu or Cu + Mg (or Si + Mg or Si + Mg + Cu) as main elements, possible minor elements such as Mn , Cr, Zr, Zn, Ag and unavoidable processing impurities such as Fe up to 1% and Si up to 1% (in 2000 alloys only in the latter case), other elements, including Li, with a maximum content of 0.05% each and 0.15% in total. (Unless otherwise indicated, the compositions refer to the weight content).
On sait que pour l'utilisation finale, les alliages concernés sont mis en solution, trempés, éventuellement écrouis par déformation contrôlée et mûris et/ou revenus. A cet état, ces alliages sont sensibles à la corrosion intercristalline, ce qui limite leur emploi dans les conditions agressives, en particulier en atmosphère marine pour des expositions longues.It is known that for the end use, the alloys concerned are dissolved, quenched, possibly hardened by controlled deformation and cured and / or tempered. In this state, these alloys are sensitive to intercrystalline corrosion, which limits their use in aggressive conditions, in particular in a marine atmosphere for long exposures.
On sait que les alliages de la série 6000, en particulier ceux qui contiennent du Cu et notamment au-delà de Cu = 0,3%, sont sensibles à la CI, mais qu'ils ne sont pas sensibles à la corrosion sous tension. Les alliages de la série 2000 peuvent, dans certaines conditions, être sensibles à la CI sans être sensibles à la corrosion sous tension. Ceci est néfaste, non seulement au point de vue aspect de surface, mais aussi parce que les défauts induits par la CI peuvent constituer des amorces de propagation des fissures de fatigue, même en l'absence de corrosion sous tension.It is known that the alloys of the 6000 series, in particular those which contain Cu and in particular beyond Cu = 0.3%, are sensitive to CI, but that they are not sensitive to corrosion under stress. Alloys of the 2000 series can, under certain conditions, be sensitive to IC without being sensitive to corrosion under stress. This is harmful, not only from the point of view of surface appearance, but also because the defects induced by the IC can constitute primers for the propagation of fatigue cracks, even in the absence of corrosion under stress.
Il est donc souhaitable d'améliorer la résistance à la CI de ces alliages.It is therefore desirable to improve the CI resistance of these alloys.
Le procédé selon l'invention consiste, dans la gamme de traitement thermique de ces alliages, à pratiquer une mise en solution dans un domaine de températures situé de 10 à 100°C en-dessous de la température de mise en solution classique (Tms).The method according to the invention consists, in the range of heat treatment of these alloys, in practicing a solution in a temperature range located from 10 to 100 ° C below the conventional solution temperature (Tms) .
Pour les alliages de la série 2000, utilisés aux états T3xx, T4, T8 ou T8xx, ce domaine de températures est de préférence tenu de 10 à 30°C au-dessous de Tms.
Pour les alliages de la série 6000, en particulier pour les alliages 6013 ou 6056, utilisés aux états T6, T6xx ou sous-revenus ou livrés aux états T3xx ou T4, il est tenu de 10 à 100°C au-dessous de Tms.For alloys of the 2000 series, used in states T3xx, T4, T8 or T8xx, this temperature range is preferably kept from 10 to 30 ° C below Tms.
For 6000 series alloys, in particular for alloys 6013 or 6056, used in T6, T6xx or under-income states or delivered in T3xx or T4 states, it is required from 10 to 100 ° C below Tms.
Les états T ci-dessus sont conformes à la nomenclature de l'Aluminum Association.The T statements above are in accordance with the nomenclature of the Aluminum Association.
La température de mise en solution Tms est connue de l'homme du métier.The Tms solution temperature is known to those skilled in the art.
En pratique, la mise en solution classique est effectuée à une température située de 5 à 10°C en-dessous de la température de fusion des eutectiques. Elle est généralement indiquée dans les ouvrages de référence tels que :
Metal Handbook- 8th Edition, Vol.2, 1964, p.272
Aluminum, Vol.III, Fabrication and Finishing, K.R Van HORN Ed. ASM, 1967.In practice, the conventional dissolution is carried out at a temperature situated from 5 to 10 ° C. below the melting point of the eutectics. It is generally indicated in reference works such as:
Metal Handbook- 8th Edition, Vol.2, 1964, p.272
Aluminum, Vol.III, Fabrication and Finishing, KR Van HORN Ed. ASM, 1967.
Elle peut cependant être déterminée expérimentalement par analyse métallographique à partir d'échantillons mis en solution à diverses températures et trempés énergiquement ou par analyse enthalpique différentielle ou AED; cette température de mise en solution correspond généralement à l'obtention d'une solution solide la plus saturée en éléments durcissants, compatible avec la composition chimique de l'alliage considéré et les contraintes pratiques des traitements thermiques industriels.It can however be determined experimentally by metallographic analysis from samples dissolved in various temperatures and vigorously quenched or by differential enthalpy analysis or AED; this dissolution temperature generally corresponds to obtaining a solid solution most saturated with hardening elements, compatible with the chemical composition of the alloy considered and the practical constraints of industrial heat treatments.
La société demanderesse a remarqué que les produits désensibilisés à la CI pouvaient être caractérisés par deux paramètres physiques, pris individuellement ou en combinaison. Il s'agit de la conductivité électrique superficielle et du signal AED.
La conductivité électrique superficielle des alliages selon l'invention est supérieure d'au moins 0,7 MS/m à celle des alliages selon l'art antérieur traités dans des conditions analogues, sauf en ce qui concerne la température de mise en solution.The applicant company noted that the products desensitized to IC could be characterized by two physical parameters, taken individually or in combination. This is the conductivity electrical surface and AED signal.
The surface electrical conductivity of the alloys according to the invention is at least 0.7 MS / m higher than that of the alloys according to the prior art treated under analogous conditions, except as regards the solution temperature.
L'énergie associée du pic AED relatif à la fusion des eutectiques des alliages suivant l'invention, déterminée dans les conditions reportées ci-après, est supérieure d'au moins 3 J/g (en valeur absolue) à celle relative au pic correspondant des alliages classiques.
Les thermogrammes AED sont tracés à une vitesse de chauffage de 20°C/min sur des échantillons de 50 mg environ (appareil PERKIN ELMER DSC7).The energy associated with the AED peak relating to the fusion of the eutectics of the alloys according to the invention, determined under the conditions reported below, is at least 3 J / g (in absolute value) greater than that relating to the corresponding peak classic alloys.
The AED thermograms are plotted at a heating rate of 20 ° C / min on samples of approximately 50 mg (PERKIN ELMER DSC7 device).
L'invention sera mieux comprise à l'aide des exemples suivants, illustrés par les fig. 1 à 5.
- Les figures 1 et 2 représentent, en coupe micrographique perpendiculaire au sens long, le faciès de corrosion * de tôles en 6013 traité selon l'invention (fig. 1) ou suivant l'art antérieur (fig. 2), en surface au grandissement x 200.
- Les figures 3 à 5 représentent les tracés des thermogrammes AED des
0,1 et 2 de l'Exemple 1.échantillons
* Selon le test interne "Interano" qui consiste essentiellement en une attaque électrolytique de l'échantillon pendant 6 h sous 1 mA/cm² dans une solution électrolytique à la température ambiante contenant
- Figures 1 and 2 represent, in micrographic section perpendicular to the long direction, the corrosion facies * of sheets made of 6013 treated according to the invention (fig. 1) or according to the prior art (fig. 2), on the surface at magnification x 200.
- FIGS. 3 to 5 represent the plots of the AED thermograms of samples 0.1 and 2 of Example 1.
* According to the internal "Interano" test which essentially consists of an electrolytic attack on the sample for 6 h under 1 mA / cm² in an electrolytic solution at room temperature containing 2M NaClO₄ 0.1 / 3M AlCl₃ and 0.01 M CrO₄ (NH₄) ₂.
Une tôle en 2024 de 2000 x 1000 x 26 mm d'épaisseur brute de laminage à chaud, obtenue à partir d'un plateau coulé et homogénéisé dans les conditions habituelles, de composition chimique suivante : 0,107% Si; 0,198% Fe; 4,39% Cu; 0,645% Mn; 1,39% Mg; 0,014% Ti; 0,01% Zr; reste Al, a été mise en solution dans les conditions suivantes : 1h à 495, 480 et 470°C avant trempe à l'eau froide et mûrie plus de 48h à l'ambiante. La première température (495°C) correspond à la mise en solution "classique" de l'alliage.A sheet in 2024 of 2000 x 1000 x 26 mm in gross thickness of hot rolling, obtained from a cast plate and homogenized under the usual conditions, with the following chemical composition: 0.107% Si; 0.198% Fe; 4.39% Cu; 0.645% Mn; 1.39% Mg; 0.014% Ti; 0.01% Zr; stay Al, was dissolved under the following conditions: 1 hour at 495, 480 and 470 ° C before quenching in cold water and matured for more than 48 hours at room temperature. The first temperature (495 ° C) corresponds to the "classic" solution of the alloy.
On a déterminé sur celle-ci les caractéristiques mécaniques dans le sens travers-long (TL), la résistance à la corrosion intercristalline dans les conditions de la norme AIR 9048, ainsi que la résistance à la corrosion sous tension par immersion-émersion (10/50 min) suivant la norme ASTM G47 sous 300 MPa (sens TL) ainsi que la ténacité apparente Kq dans le sens L-T (effort sens long et propagation sens TL).The mechanical characteristics in the cross-long direction (TL), the resistance to intercrystalline corrosion under the conditions of the AIR 9048 standard, as well as the resistance to corrosion under tension by immersion-emersion (10) were determined thereon. / 50 min) according to ASTM G47 standard at 300 MPa (TL direction) as well as the apparent toughness Kq in the LT direction (long direction force and TL direction propagation).
Les résultats obtenus sont donnés dans le Tableau I. On constate que les traitements 1 et 2 selon l'invention améliorent considérablement la tenue à la CI, tant en ce qui concerne le faciès d'attaque (passage d'une attaque intercristalline et par piqûre avec ramifications intercristallines à une attaque par, piqûre sans ramification) que la profondeur des piqûres (en µm).
Par ailleurs, les caractéristiques de résistance mécanique et de ténacité sont très peu affectées (pour le traitement à 480°C par exemple, R0,2 chute seulement de 3,5%, Kq chute de 3,6%). On constate de plus que la résistance à la corrosion sous contrainte (CSC) est aussi très améliorée.The results obtained are given in Table I. It can be seen that the
Furthermore, the characteristics of mechanical resistance and toughness are very little affected (for the treatment at 480 ° C. for example, R0.2 drops only 3.5%, Kq drops 3.6%). It can also be seen that the resistance to stress corrosion (CSC) is also greatly improved.
Une tôle de 2000 x 1000 mm en alliage 6013 de composition en poids : 0,82% Si; 0,22% Fe; 0,92% Cu; 0,9% Mg; 0,62% Mn; 0,15% Zn; ≦ 0,08% Ti et d'épaisseur 6 mm a été mise en solution dans les conditions rapportées au Tableau II, opération suivie d'une trempe à l'eau froide, d'une maturation de deux jours et d'un revenu du type T6 (6 heures à 175°C). Une comparaison est faite avec une mise en solution classique (30 minutes à 550°C), suivie d'une trempe à l'eau froide, d'une maturation de deux jours et d'un revenu du type T6 (6 heures à 175°C).A 2000 x 1000 mm sheet of alloy 6013 with a composition by weight: 0.82% Si; 0.22% Fe; 0.92% Cu; 0.9% Mg; 0.62% Mn; 0.15% Zn; ≦ 0.08% Ti and 6 mm thick was dissolved under the conditions reported in Table II, operation followed by quenching in cold water, two days maturation and tempering of the type T6 (6 hours at 175 ° C). A comparison is made with a conventional solution treatment (30 minutes at 550 ° C.), followed by quenching in cold water, two days maturation and an income of the T6 type (6 hours at 175 ° C).
Les propriétés obtenues dans les deux cas sont reportées dans le Tableau II. Après test de corrosion intercristalline (selon la norme interne Interano*) des caractérisations en microscopie optique ont été effectuées : les modes de corrosion observés (intercristalline, piqûres (transgranulaires), ou piqûres avec ramifications intercristallines) ainsi que les profondeurs maximales d'attaque (en µm) et les proportions de la surface attaquées estimées à partir des coupes micrographiques sont également reportées.The properties obtained in the two cases are reported in Table II. After intercrystalline corrosion test (according to internal standard Interano *) characterizations in light microscopy were carried out: the corrosion modes observed (intercrystalline, pitting (transgranular), or pitting with intercrystalline ramifications) as well as the maximum depths of attack (in µm) and the proportions of the attacked surface estimated from micrographic sections are also reported.
On constate que les alliages traités suivant l'invention possèdent une résistance à la corrosion intercristalline sensiblement améliorée par rapport à celle de ceux obtenus selon l'art antérieur.It is found that the alloys treated according to the invention have a resistance to intercrystalline corrosion substantially improved compared to that of those obtained according to the prior art.
Les alliages obtenus suivant l'invention sont utilisables notamment dans le domaine des industries de la construction mécanique et des transports (ferroviaire, automobile, aéronautique, maritime).
Claims (9)
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR9311861A FR2710657B1 (en) | 1993-09-28 | 1993-09-28 | Desensitization process for intercrystalline corrosion of Al alloys 2000 and 6000 series and corresponding products. |
FR9311861 | 1993-09-28 |
Publications (1)
Publication Number | Publication Date |
---|---|
EP0645467A1 true EP0645467A1 (en) | 1995-03-29 |
Family
ID=9451554
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP94420256A Withdrawn EP0645467A1 (en) | 1993-09-28 | 1994-09-26 | Process for desensitization to intercristalline corrosion of alumium alloys of the series 2000 and 6000, and articles made according to this process |
Country Status (7)
Country | Link |
---|---|
US (1) | US5643372A (en) |
EP (1) | EP0645467A1 (en) |
JP (1) | JPH07180004A (en) |
KR (1) | KR950008711A (en) |
AU (1) | AU680014B2 (en) |
CA (1) | CA2130766A1 (en) |
FR (1) | FR2710657B1 (en) |
Families Citing this family (9)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR2726007B1 (en) * | 1994-10-25 | 1996-12-13 | Pechiney Rhenalu | PROCESS FOR PRODUCING ALSIMGCU ALLOY PRODUCTS WITH IMPROVED INTERCRYSTALLINE CORROSION RESISTANCE |
US7275582B2 (en) * | 1999-07-29 | 2007-10-02 | Consolidated Engineering Company, Inc. | Methods and apparatus for heat treatment and sand removal for castings |
US7338629B2 (en) * | 2001-02-02 | 2008-03-04 | Consolidated Engineering Company, Inc. | Integrated metal processing facility |
CN1526027A (en) * | 2001-02-02 | 2004-09-01 | ̹�� | Integrated metal processing facility |
WO2004009855A1 (en) * | 2002-07-18 | 2004-01-29 | Consolidated Engineering Company, Inc. | Method and system for processing castings |
US20060054294A1 (en) * | 2004-09-15 | 2006-03-16 | Crafton Scott P | Short cycle casting processing |
US20060103059A1 (en) * | 2004-10-29 | 2006-05-18 | Crafton Scott P | High pressure heat treatment system |
EP2489452A3 (en) * | 2007-03-29 | 2013-05-01 | Consolidated Engineering Company, Inc. | System and method for forming and heat treating metal castings |
JP6743132B2 (en) | 2015-04-28 | 2020-08-19 | コンソリデイテット エンジニアリング カンパニー,インコーポレイテッド | System and method for heat treating aluminum alloy castings |
Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR1463418A (en) * | 1965-03-04 | 1966-12-23 | Ver Leichtmetallwerke Gmbh | Process for improving the resistance to stress corrosion of forged and forged parts in aluminum alloys sensitive to this type of corrosion |
GB1306206A (en) * | 1971-03-16 | 1973-02-07 | ||
FR2278785A1 (en) * | 1974-01-07 | 1976-02-13 | Pechiney Aluminium | PROCESS FOR REINFORCING THE MECHANICAL CHARACTERISTICS OF HEAT-TREATED ALUMINUM ALLOYS AND PRODUCTS THUS OBTAINED |
FR2293497A2 (en) * | 1974-12-04 | 1976-07-02 | Pechiney Aluminium | Stress-corrosion resistant aluminium alloys - obtd. by overageing after homogenising have good mechanical properties |
FR2333053A1 (en) * | 1975-11-25 | 1977-06-24 | Cegedur | PROCESS FOR THE PREPARATION OF ALUMINUM SHEETS INTENDED TO BE WELDED, WITH IMPROVED CORROSION RESISTANCE |
FR2370105A2 (en) * | 1976-11-08 | 1978-06-02 | Cegedur | Weldable aluminium alloy sheet - with good mechanical properties and very high corrosion resistance |
Family Cites Families (3)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
BE639908A (en) * | 1962-11-15 | |||
US3305410A (en) * | 1964-04-24 | 1967-02-21 | Reynolds Metals Co | Heat treatment of aluminum |
US3198676A (en) * | 1964-09-24 | 1965-08-03 | Aluminum Co Of America | Thermal treatment of aluminum base alloy article |
-
1993
- 1993-09-28 FR FR9311861A patent/FR2710657B1/en not_active Expired - Fee Related
-
1994
- 1994-08-15 US US08/290,534 patent/US5643372A/en not_active Expired - Fee Related
- 1994-08-24 CA CA002130766A patent/CA2130766A1/en not_active Abandoned
- 1994-08-26 AU AU71495/94A patent/AU680014B2/en not_active Expired - Fee Related
- 1994-09-13 KR KR1019940022988A patent/KR950008711A/en not_active Application Discontinuation
- 1994-09-26 EP EP94420256A patent/EP0645467A1/en not_active Withdrawn
- 1994-09-28 JP JP6233608A patent/JPH07180004A/en active Pending
Patent Citations (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
FR1463418A (en) * | 1965-03-04 | 1966-12-23 | Ver Leichtmetallwerke Gmbh | Process for improving the resistance to stress corrosion of forged and forged parts in aluminum alloys sensitive to this type of corrosion |
GB1306206A (en) * | 1971-03-16 | 1973-02-07 | ||
FR2278785A1 (en) * | 1974-01-07 | 1976-02-13 | Pechiney Aluminium | PROCESS FOR REINFORCING THE MECHANICAL CHARACTERISTICS OF HEAT-TREATED ALUMINUM ALLOYS AND PRODUCTS THUS OBTAINED |
FR2293497A2 (en) * | 1974-12-04 | 1976-07-02 | Pechiney Aluminium | Stress-corrosion resistant aluminium alloys - obtd. by overageing after homogenising have good mechanical properties |
FR2333053A1 (en) * | 1975-11-25 | 1977-06-24 | Cegedur | PROCESS FOR THE PREPARATION OF ALUMINUM SHEETS INTENDED TO BE WELDED, WITH IMPROVED CORROSION RESISTANCE |
FR2370105A2 (en) * | 1976-11-08 | 1978-06-02 | Cegedur | Weldable aluminium alloy sheet - with good mechanical properties and very high corrosion resistance |
Also Published As
Publication number | Publication date |
---|---|
AU680014B2 (en) | 1997-07-17 |
US5643372A (en) | 1997-07-01 |
KR950008711A (en) | 1995-04-19 |
AU7149594A (en) | 1995-04-13 |
FR2710657A1 (en) | 1995-04-07 |
JPH07180004A (en) | 1995-07-18 |
CA2130766A1 (en) | 1995-03-29 |
FR2710657B1 (en) | 1995-11-10 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
CN1237195C (en) | Weldable high strength Al-Mg-Si alloy product | |
EP0162096B1 (en) | Aluminium alloys containing lithium, magnesium and copper | |
EP0679199B1 (en) | Aluminium-silicon-magnesium alloy having improved ductility and deep-drawing properties, and method for producing same | |
WO2015098484A1 (en) | Aluminum alloy plate for molding | |
EP0008996B1 (en) | Process for heat-treating aluminium-copper-magnesium-silicon alloys | |
EP0756017B1 (en) | Aluminium-copper-magnesium alloy with high creep resistance | |
JP2006009140A (en) | 6000 series aluminum alloy sheet having excellent hardenability of coating/baking and production method therefor | |
JP2012001756A (en) | HIGH-TOUGHNESS Al ALLOY FORGING MATERIAL, AND METHOD FOR PRODUCING THE SAME | |
EP0645467A1 (en) | Process for desensitization to intercristalline corrosion of alumium alloys of the series 2000 and 6000, and articles made according to this process | |
JP2011202284A (en) | Method for producing 6000 series aluminum alloy sheet having excellent paint bake hardenability and production method therefor | |
EP0227563B1 (en) | Process od desensitization to exfoliating corrosion of lithium-containing aluminium alloys, resulting simultaneously in a high mechanical resistance and in good damage limitation | |
JP4111651B2 (en) | Al-Mg-Si aluminum alloy extruded material for door beam and door beam | |
EP0388283B1 (en) | Stainless ferritic steel and process for manufacturing this steel | |
JPH06340940A (en) | Aluminum alloy sheet excellent in press formability and baking hardenability and its production | |
EP0282421A2 (en) | Aluminium alloy product containing lithium resistant to corrosion under tension and process for production | |
RU2165996C1 (en) | Highly strong aluminium-based alloy and product thereof | |
JPH08269608A (en) | High strength aluminum alloy excellent in formability and corrosion resistance | |
JPH10259464A (en) | Production of aluminum alloy sheet for forming | |
JP2006241548A (en) | Al-Mg-Si ALLOY SHEET SUPERIOR IN BENDABILITY, MANUFACTURING METHOD THEREFOR, AND AUTOMOTIVE SKIN PLATE OBTAINED FROM THE SHEET | |
EP0394155A1 (en) | Damage resistant Al-li-cu-mg alloy having good cold-forming properties | |
EP3802897B1 (en) | Thin sheets made of aluminium-copper-lithium alloy for aircraft fuselage manufacture | |
Agboola et al. | Effects of Aging Temperature and Time on Microstructure and Mechanical Properties of LM 12 Aluminium Alloy | |
FR3132306A1 (en) | Aluminum-Copper-Lithium Alloy Enhanced Thin Sheet | |
WO2023187301A1 (en) | Recycled 6xxx alloy sheet and manufacturing process | |
FR2857377A1 (en) | Aluminium alloy for rolled products with a high capacity of absorption of kinetic energy by plastic deformation, notably for motor vehicle components |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): CH DE FR GB IT LI |
|
17P | Request for examination filed |
Effective date: 19950428 |
|
17Q | First examination report despatched |
Effective date: 19970826 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE APPLICATION IS DEEMED TO BE WITHDRAWN |
|
18D | Application deemed to be withdrawn |
Effective date: 19980106 |