6XXX ALUMINIUM ALLOY EXTRUDED FORGING STOCK AND METHOD OF MANUFACTURING THEREOF

Abstract

The invention concerns an aluminum extruded product as feedstock for forging comprising in weight percent Si: 0.6% to 1.4%, Fe: 0.01% to 0.15%, Cu: 0.05% to 0.60%, Mn: 0.4% to 1%, Mg: 0.4% to 1.2%, Cr: 0.05% to 0.25%, Zn0.2%, Ti0.1%, Zr0.05%, the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%, wherein the number density of Mn containing dispersed particles is at least equal to 2.5 particles per m.sup.2, preferably 3.0 particles per m.

The invention also concerns the process to obtain the aluminum extruded product as feedstock for forging.

Claims

1. An aluminum extruded product as feedstock for forging comprising in weight percent Si: 0.6% to 1.4%, Fe: 0.01% to 0.15%, Cu: 0.05% to 0.60%, Mn: 0.4% to 1%, Mg 0.4% to 1.2%, Cr: 0.05% to 0.25%, Zn0.2%, Ti0.1%, Zr0.05%, the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%, wherein the number density of Mn containing dispersed particles is at least equal to 2.5 particles per m.sup.2, optionally 3.0 particles per m.sup.2.

2. The aluminum extruded product as feedstock for forging according to claim 1 wherein the average diameter of Mn containing dispersed particles is less than 80 nm, optionally less than 60 nm.

3. The aluminum extruded product as feedstock for forging according to claim 1 wherein the maximum fraction of texture components belonging to the <001> fiber is 20%.

4. The aluminum extruded product as feedstock for forging according to claim 1 wherein Fe content is between 0.01 wt. % to 0.13 wt. %.

5. The aluminum extruded product as feedstock for forging according to claim 1 wherein in weight percent Si: 1.2% to 1.3% Cu: 0.05% to 0.15% Mn: 0.7% to 0.8% Mg: 0.8% to 0.9% Cr: 0.10% to 0.25%

6. The aluminum extruded product as feedstock for forging according to claim 1 wherein in weight percent Si: 0.8% to 1% Cu: 0.40% to 0.55% Mn: 0.4% to 0.6% Mg: 0.7% to 0.9% Cr: 0.10% to 0.25%

7. A process for manufacturing aluminum extrusion feedstock for forging comprising a) Casting a billet of aluminum alloy comprising in weight percent Si: 0.6% to 1.4% Fe: 0.01% to 0.15% Cu: 0.05% to 0.60% Mn: 0.4% to 1% Mg 0.4% to 1.2% Cr: 0.05%-0.25% Zn0.2% Ti0.1% Zr0.05% the rest being aluminum and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15% b) homogenizing said billet at a temperature between 480 to 560 C. for 2 to 12 hours c) extruding said homogenized billet as a solid extrusion, with an extrusion ratio less than 15, optionally less than 13, optionally as a round bar shape.

8. Process for manufacturing aluminum extrusion feedstock for forging according to claim 7 wherein the Fe content of the composition of the aluminum alloy billet casted at a) is between 0.01 wt. % to 0.13 wt. %.

9. Process for manufacturing aluminum extrusion feedstock for forging according to claim 7 wherein the composition of the aluminum alloy billet casted at step a) comprises in weight % Si: 1.2% to 1.3% Fe: 0.01% to 0.15%, optionally between 0.01% to 0.13% Cu: 0.05% to 0.15% Mn: 0.7% to 0.8%, optionally between 0.75% to 0.80%. Mg: 0.8% to 0.9%, optionally between 0.80% to 0.90%. Cr: 0.10% to 0.25% Zn0.2% Ti0.1% Zr0.05% the rest being aluminum and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%.

10. Process for manufacturing aluminum extrusion feedstock for forging according to claim 7 wherein the composition of the aluminum alloy billet casted at a) comprises in weight % Si: 0.8% to 1 wt. % Fe: 0.01% to 0.15%, optionally between 0.01% to 0.13% Cu: 0.40%-0.55% Mn: 0.4% to 0.6% Mg: 0.7% to 0.9%, optionally between 0.70% to 0.85%. Cr: 0.10% to 0.25% Zn0.2% Ti0.1% Zr0.05% the rest being aluminum and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%.

11. Process for manufacturing aluminum extrusion feedstock for forging according to claim 7 wherein homogenizing of said billet is performed at a temperature between 490 C. to 510 C. for 2 to 12 hours.

12. Process for manufacturing an aluminum forged product according to claim 7, wherein after c) forging is performed.

13. Process for manufacturing an aluminum forged product according to claim 12 wherein the homogenizing of b) is performed at a temperature between 490 to 510 C.

14. An aluminum forged product obtained by the process of claim 13, wherein the forged product presents at a thinnest location a recrystallized fraction equal or less than 50%, optionally less than 15%.

15. An aluminum forged product comprising in weight percent: Si: 1.2% to 1.3% Fe: 0.01% to 0.15%, optionally between 0.01% to 0.13% Cu: 0.05% to 0.15% Mn: 0.7% to 0.8%, optionally between 0.75% to 0.80%. Mg: 0.8% to 0.9%, optionally between 0.80% to 0.90%. Cr: 0.10% to 0.25% Zn0.2% Ti0.1% Zr0.05% the rest being aluminum and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%. obtained by the process of claim 13, wherein the forged product presents at a thinnest location an improved balance between ductility and strength with a yield strength higher than 350 MPa and an elongation higher than 13%.

Description

BRIEF DESCRIPTION OF THE DRAWINGS

[0106] FIG. 1 to FIG. 3 represents cross sections of samples representing the fibrous aspect vs. extrusion ratio, exemplified in example 2.

DETAILED DESCRIPTION OF THE INVENTION

[0107] The inventors have found that it is possible to control the recrystallization during forging by using an aluminium extrusion feedstock with the following composition in weight % [0108] Si: 0.6% to 1.4% [0109] Fe: 0.01% to 0.15% [0110] Cu: 0.05% to 0.60% [0111] Mn: 0.4% to 1% [0112] Mg: 0.4% to 1.2% [0113] Cr: 0.05% to 0.25% [0114] Zn0.2% [0115] Ti0.1% [0116] Zr0.05% [0117] the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%.

[0118] Si and Mg content are defined so as to ensure high level of dissolved Mg.sub.2Si while minimizing presence of undissolved Mg.sub.2Si in the forged component after ultimate solutionising step, with a minimum content of 0.6 wt. % of undissolved Mg.sub.2Si.

[0119] Si is combined with Mg to form Mg.sub.2Si. The precipitation of Mg.sub.2Si contributes to increasing the strength of the final aluminium alloy forged product.

[0120] If the Si content is less than 0.6 wt. %, the final product does not have a sufficiently high strength.

[0121] On the other hand, if the Si content is more than 1.4 wt. %, the level of undissolved Mg.sub.2Si is too high and extrudability is reduced as well as corrosion resistance and toughness of the resultant final forged product.

[0122] Si is comprised between 0.6 wt. % and 1.4 wt. %. In a preferred embodiment, Si content is between 1.2% and 1.4% to obtain higher strength. In another embodiment, Si content is between 0.8 wt. % and 1.0 wt. % to obtain a good balance between strength and fatigue. Mg is combined with Si to form Mg.sub.2Si. Therefore, Mg is needed for strengthening the product of the present invention. If the Mg content is lower than 0.4 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 extrude and the extruded bar also is difficult to forge. Moreover, a large amount of Mg.sub.2Si particles tends to precipitate during quenching process after the solution heat treatment.

[0123] Mg content is between 0.4 wt. % and 1.2 wt. %, preferably between 0.7 wt. % and 0.9 wt. %. In one embodiment, Mg content is between 0.70 wt. % and 0.85 wt. %. In another embodiment, Mg content is between 0.8 wt. % and 0.9 wt. %, and more preferably between 0.80 wt. % and 0.90 wt. %.

[0124] Preferably, the ratio Mg/Si is between 0.5 to 1.2, preferably between 0.5 to 0.8.

[0125] Mn and Cr produce dispersed particles, which are formed during homogenization.

[0126] Dispersed particles with a sufficient number density per unit area prevent recrystallization during forging. Mn containing dispersed particles are preferred to prevent recrystallization due to a more homogeneous distribution within grains. Cr dispersed particles are complementary to Mn containing dispersed particles to enhance recrystallization resistance, but they present a more localized particle distribution due to Cr behavior during solidification reactions.

[0127] 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. Coarse precipitated particles are also detrimental to preventing recrystallization. The Mn content is preferably between 0.4 wt. % and 0.8 wt. % and more preferably between 0.7 wt. % and 0.8 wt. %. In a preferred embodiment, Mn is in the range of 0.4% to 0.6% and in another embodiment, Mn is in the range of 0.7% to 0.8%.

[0128] If the Cr is less than 0.05 wt. %, preferably less than 0.10 wt. % the effect is not sufficient. If the content of Cr is higher than 0.25 wt. % coarse precipitated particles are formed and both the workability and the toughness of the aluminium alloy are reduced. Coarse precipitated particles are also detrimental to preventing recrystallization.

[0129] Fe combines with other elements, such as Mn and Cr, and may form dispersed particles and iron containing intermetallic particles.

[0130] Iron containing intermetallic particles are formed during casting and differ from Mn containing dispersed particles by higher dimension and stoichiometric chemical compositions.

[0131] The amount and the size of iron containing intermetallic particles should be restricted to enhance fatigue properties. It can be achieved by reducing Fe content. However, Fe is also known to be beneficial for grain structure control by preventing grain boundary migration after recrystallization, preventing coarsening of crystal grains and refining the grains, and a minimum content of about 0.15 wt. % is common. To the contrary, the inventors found that unexpectedly if the Fe content is kept in the range of 0.01 wt. % to 0.15 wt. %, preferably between 0.01 wt. % to 0.13 wt. %, more preferably between 0.01 wt. % to 0.12 wt. %, and even more preferably between 0.01 wt. % to 0.10 wt. % or between 0.01 wt. % to 0.08 wt. %, recrystallization can be prevented without adverse effects on the grain structure.

[0132] The present inventors found that when the Fe content is too high a detrimental effect for the formation of Mn containing dispersed particles is observed.

[0133] Although they are not bound to any theory, the inventors believe that low Fe content ensures a sufficient concentration of free Mn to permit the formation of Mn containing dispersed particles.

[0134] Fe content is interesting to be kept at a minimum of 0.01 wt %, preferably 0.02 wt. % and more preferably 0.05 wt %.

[0135] Cu content is between 0.05 wt. % to 0.60 wt. %. Cu strengthens the forged product. When the Cu content is too low, this effect cannot be obtained. On the other hand, if the Cu content is too high the alloy becomes sensitive to intergranular corrosion. Also, if the Cu content is too high, the extrudability is reduced. Preferably, Cu content is in the range of 0.05 wt. % to 0.55 wt. %, preferably between 0.15 wt. % to 0.55 wt. % and even more preferably between 0.40 to 0.55 wt. %. In a preferred embodiment, Cu is in the range of 0.05% to 0.15% and in another embodiment Cu is in the range of 0.40% to 0.55%.

[0136] Ti content is below 0.1 wt. %. Ti is a grain refiner to improve the resistance to hot cracking in the alloy and workability of the extruded product. Preferably, Ti content is at least 0.01 wt. %. When Ti exceeds 0.1 wt. %, the workability is deteriorated due to coarse precipitates.

[0137] Zr content is kept below 0.05 wt %. If the content of Zr is too high, the extrudability of the product is reduced. In addition, a too high Zr content can be detrimental to ductility and fatigue by the formation of primary crystals.

[0138] Zn content is equal or less to 0.2%. Zn can precipitate with Mg to form MgZn.sub.2 during artificial aging treatment. It permits to increase the strength of the forged product. If Zn is too high, it can induce corrosion sensitivity.

[0139] In the present invention, Mn containing dispersed particles, also called Mn containing dispersoids particles are dispersed particles formed during homogenization. Mn containing dispersed particles are combination of Al, Mn, Fe, Si, Cr elements, such as AlMn, AlMnFe, AlCrMn or AlMnFeSi composed dispersed particles. For instance, Al.sub.15 (Mn,Fe).sub.3Si.sub.2 or Ali.sub.2CrMn can be present in the extruded feedstock.

[0140] Mn containing dispersed particles are formed at high temperature, typically higher than 480 C. They are preferably formed during the homogenizing treatment. Preferably, the homogenizing treatment is performed at a temperature between 480 to 560 C. during 2 to 12 hours. More preferably, the homogenizing treatment is performed at a temperature between 490 C. to 510 C., i.e 500 C.+/10 C. during 2 to 12 hours. It is advantageous that before forging a sufficient number density of Mn containing dispersed particles are present in the extruded feedstock. Depending on forging conditions, the number density of Mn containing dispersed particles can be unchanged or increase or decrease depending on dissolution/re-precipitation/precipitation phenomena.

[0141] Dispersed particles affect the recrystallization behavior. When dispersed particles are fine and at a high density, they can obstruct the grain boundary movement during recrystallization and prevent coarsening of the crystal grain. This is also known as the Zener drag effect. The density or number density of Mn containing dispersed particles per unit area affects the susceptibility of the forged product for recrystallization. When the number density of Mn containing dispersed particles is higher than 2.5 per m.sup.2, recrystallization is decreased. This effect is more pronounced if the number density of Mn containing dispersed particles is higher than 3.0 per m.sup.2.

[0142] When the average diameter of Mn containing dispersed particles is lower than 80 nm, preferably lower than 60 nm and even more preferably lower than 50 nm, recrystallization is reduced.

[0143] Re-precipitation or dissolution of Mn containing dispersed particles are unwanted during forging and subsequent thermal treatment to maintain a homogeneous distribution of Mn containing dispersed particles.

[0144] The number density of Mn containing dispersed particles per unit area and the average diameter of Mn containing dispersed particles (D.sub.circle) are determined by using high resolution techniques such as TEM or SEM. EDX is associated to chemically identify the Mn containing dispersed particles. Image analysis is preferably implemented to have an automated treatment permitting to directly plot the dispersed distribution (number of Mn containing dispersed particles vs diameter, number of Mn containing dispersed particles vs surface area). SEM observations associated with images analysis provide a good representativeness of the sampling. The results are preferably based on at least 200 images done at high magnification (typical magnification above 20000, preferentially above 30000) covering a total analyzed surface of at least 5000 m.sup.2. It permits to cover a significant area of the product without the disadvantage of treating high amounts of data.

[0145] The number density of Mn containing dispersed particles corresponds to the ratio between the total number of Mn containing dispersed particles, which have been identified by image analysis (for instance by a threshold of grey level set to discriminate aluminum matrix with Mn containing dispersed particles), and the total analysed surface.

[0146] The average diameter of Mn containing dispersed particles corresponds to the average D.sub.circle. It must be understood that by the diameter of Mn containing dispersed particles, one wants to say equivalent diameter, i.e. that of a particle which would be of circular section and would have the same surface as the particle observed, if this one has a section more complex than that of a simple circle. The average D.sub.circle corresponds to the equivalent diameter of the circle having the same surface as the average surface of all the Mn containing dispersed particles.

[0147] It is also possible with the image analysis to determine the surface fraction area. It corresponds to the ratio between the total surface covered by Mn containing dispersed particles and the total analyzed surface.

[0148] Aluminum extruded product as feedstock for forging differ from most extruded by their plain cross-section, i.e. they are solid extrusions, which typically have a simple shape such as a round, rectangle or square. Compared for example to cast feedstock, extruded products are advantageous as feedstock for forging, in particular for relatively small forgings, as they allow the manufacturing of near-net shape parts with higher precision, typically forged products with a total width lower than 50 cm and section with thickness lower than 10 mm. Since the parts in question undergo elevated working rates at critical sections (e.g. aiming at achieving a thinner web thickness), the use of extruded products for forging offers the possibility of reducing the number of deformation passes, therefore restricting the higher strain levels loaded in the thinnest portions of the forged product.

[0149] The refined microstructure is further achieved by properly designing the temperature and strain rate schedules both during the extrusion process and forging to favor dynamic recovery over recrystallization.

[0150] Moreover, the fibrous microstructure obtained in the feedstock through the extrusion process can be retained during forging, thus ensuring that a fine substructure is achieved in the forged end product, which is beneficial for higher strength as well as fatigue properties.

[0151] The inventors found that to ensure a satisfying balance between strength, ductility and fatigue for specific forged products, the maximum fraction of texture components belonging to the <001> fiber is 20%. Surprisingly, the inventors found that by controlling the extrusion ratio below 15, preferably below 13, the <001> fiber texture surface fraction in the extrusion feedstock is limited while <111> fiber texture surface fraction remains higher than 70%. By decreasing the extrusion ratio, recrystallization can be then limited during subsequent deformation. Indeed, limiting <001> fiber texture is supposed to inhibit the formation of potential nuclei for the further development of e.g., Cube recrystallization texture in the end product during subsequent thermomechanical processing steps.

[0152] The fraction of texture components belonging to the <001> fiber texture is measured using orientation imaging microscopy (OIM). When the electron beam in a Scanning Electron Microscope (SEM) strikes a crystalline material mounted at an inclined surface (e.g., around 70), the electrons disperse beneath the surface, subsequently diffracting among the crystallographic planes. The diffracted beam produces a pattern composed of intersecting bands, termed electron backscatter patterns, or EBSPs. EBSPs can be used to determine the orientation of the crystal lattice with respect to some laboratory reference frame in a material of known crystal structure.

[0153] Fraction of <001> fiber components means the area fraction of texture components belonging to the <001> fiber oriented grains of a given polycrystalline sample as calculated using orientation imaging microscopy using, for example, the EBSD measurements, described in example 2. Within the <001> family, Cube orientation {001}<100>, Goss orientation {011}<100>, rotated Goss {021}<100> as major texture components can be cited.

[0154] The forged parts are subjected to dynamic loading conditions over its service life, thus requiring superior fatigue properties, which can only be delivered by a very fine grains structure. A fine substructure is also beneficial for improving corrosion resistance.

[0155] By contrast, it has been observed that cast feedstock do not allow the desired refinement of the microstructure.

[0156] Example J of EP 2003219 is a good illustration of this statement. Despite a low Fe content (0.02 wt. %), the forged product obtained from the cast feedstock exhibits 100% of recrystallization in the rib structure. EP 2003219 attributed this effect to the too low Fe content, which does not encourage reducing Fe level.

[0157] A process for producing the aluminium extruded feedstock for forging according to the invention is described.

[0158] Casting a billet of aluminum alloy comprising in weight percent: [0159] Si: 0.6% to 1.4% [0160] Fe: 0.01% to 0.15%, preferably between 0.01% to 0.13%, more preferably between 0.01% to 0.12% and even more preferably between 0.01% to 0.10%. [0161] Cu: 0.05% to 0.60% [0162] Mn: 0.4% to 1% [0163] Mg 0.4% to 1.2% [0164] Cr: 0.05% to 0.25% [0165] Zn0.2% [0166] Ti0.1% [0167] Zr0.05% [0168] the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%.

[0169] Casting is performed using DC casting or hot top casting.

[0170] Said cast billet is homogenized. Homogenizing is done at a temperature ranging from 480 C. to 560 C. during 2 to 12 hours, preferably between 480 C. to 545 C. It can be done in single or multiple steps. Preferably, the homogenizing temperature is in the range of 490 C. to 510 C. during 2 to 12 hours to permit to obtain thin Mn containing dispersed particles, typically Mn containing dispersed particles with an average diameter of less than 50 nm.

[0171] Said homogenized billet is extruded as a solid extrusion, with an extrusion ratio less than 15. Preferably the solid extrusion is a round bar shape. Preferably the extrusion ratio is less than 13.

[0172] The extrusion ratio is defined by the ratio between the section of the press container and the section of the extrusion.

[0173] An extrusion ratio less than 15 permits to increase the number density of Mn containing dispersed particles ensuring a better efficiency to prevent recrystallization during forging or subsequent deformation. Contrary to what was cited in EP2644727, an extrusion ratio lower than 15 permits to retain a fibrous microstructure.

[0174] Preferably the composition of step a) comprises in wt. % [0175] Si: 1.2% to 1.3% [0176] Fe: 0.01 to 0.15%, preferably between 0.01% to 0.13% [0177] Cu: 0.05% to 0.15% [0178] Mn: 0.7% to 0.8%, preferably between 0.75% to 0.80%. [0179] Mg: 0.8% to 0.9%, preferably between 0.80% to 0.90%. [0180] Cr: 0.10% to 0.25% [0181] Zn0.2% [0182] Ti0.1% [0183] Zr0.05% [0184] the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15% The combination of this preferred composition with an homogenization between 490 C. to 510 C. during 2 to 12 hours and an extrusion ratio less than 15, preferably less than 13 permits to obtain an extruded feedstock permitting to obtain on the forged product a good balance between ductility and strength with a yield strength higher than 350 MPa and an elongation higher than 13%.

[0185] In another embodiment, the composition of step a) comprises in wt. % [0186] Si: 0.8% to 1 wt. % [0187] Fe: 0.01 to 0.15%, preferably between 0.01% to 0.13% [0188] Cu: 0.40%-0.55% [0189] Mn: 0.4% to 0.6% [0190] Mg: 0.7% to 0.9%, preferably between 0.70% to 0.85%. [0191] Cr: 0.10% to 0.25% [0192] Zn0.2% [0193] Ti0.1% [0194] Zr0.05% [0195] the rest being aluminium and unavoidable impurities having a content of less than 0.05% each, total being less than 0.15%.

[0196] The process for producing the forged product from the extruded product feedstock can be performed by preforming so that it has a volume distribution resembling the finished product and then, by forging the preformed workpiece in multiple stages. In a preferred embodiment, preforming consists in two pass rolling and bending and forging has intermediate reheating steps at temperature above 500 C.

[0197] The forged product is either produced in T5 temper and then artificially aged or produced in T6 or T7 temper with a separate solution heat treatment and artificially aged after final forging steps.

[0198] By separate solution heat treatment, it is meant that the final forged product in its final shape is thermally treated in a furnace, and not solution heat treated by the heat induced during forging as can be obtained when the product is produced in a T5 temper.

[0199] The recrystallized fraction is measured on the forged product, preferably in the portion where recrystallization is more likely occurring, i.e. in the most deformed area. In an H shape form, the most distorted area is located in the web part where the thickness is the lowest. It is advantageous to reduce recrystallization in this area as it reduces mechanical strength and fatigue properties. This is particularly advantageous when the web thickness of the forged product is less than 8 mm, preferably less than 7 mm and more preferably less than 6 mm.

[0200] A forged product obtained from an extrusion feedstock produced according to the invention presents a recrystallization fraction to less than 50%, in the thinnest part of the forged product.

[0201] The recrystallization fraction less than 50% is preferably obtained when the cast billet is homogenized at a temperature between 490 C. and 510 C. during 2 to 12 hours.

[0202] If the forged product is produced in T5, i.e. not submitted to a separate heat solution treatment, the recrystallization fraction is less than 15% in the thinnest part of the forged product. The recrystallization fraction less than 15% is preferably obtained when the cast billet is homogenized at a temperature between 490 C. and 510 C. during 2 to 12 hours.

EXAMPLES

Example 1

[0203] Two billets of diameter 368 mm have been cast with a composition corresponding to alloy C according the invention (see Table 1 Error! Reference source not found.).

TABLE-US-00001 TABLE 1 composition in weight % Si Fe Cu Mn Mg Cr Zn Ti V Zr C Inv. 1.3 0.12 0.07 0.8 0.9 0.16 0.05 0.05 0.05 0.05

[0204] The as-cast billets were subsequently homogenized at a temperature of 500 C. for 4 h.

[0205] The homogenized logs were heated to 515 C. and extruded using either a 3-hollow die (extrusion ratio 21.7) to form bars with a diameter of 45 mm, or a 5-hollow die to form bars with a diameter of 45 mm (extrusion ratio of 13.4). The extruded bars exiting from the extrusion press were water quenched.

[0206] The bars, delivered in the as-quenched condition, were then submitted to 2 steps of rolling and subsequently to standard forging operation in several forging steps and intermediate heat treatments (typically at temperatures above 500 C.) to produce a H shape whose thickness in the thinner area (web) was 5.4 mm with a total width of 39 mm. Said H shape is dissymmetric and presents a height of 16.4 mm on one side and a height of 9.4 mm on the other side. The forged parts produced in T5 temper were submitted to artificial ageing at 170 C. for 8 h. The forged parts were tensile testedthe results are in Table 2.

TABLE-US-00002 TABLE 2 Mechanical Properties Homogenization Extrusion Mechanical Properties Alloy treatment ratio Rm (MPa) Rp0.2 (MPa) A (%) C 500 C./4 h 22 372 346 11.7 13 375 353 14.4

Example 2

[0207] In this example, three alloys E, F, G were cast into billets of diameter 360 mm. The composition of these alloys is listed in Table 3. The logs were homogenized at a temperature (MT) of 500 C. for 5 h. The logs were heated to 515 C. and extruded on indirect extrusion press to form bars and different diameters by varying die diameter and number of hollows, therefore producing the different extrusion ratios as given in Table 3.

[0208] The extruded bars exited from the extrusion press at extrusion speeds between 6-8 m/min and were water quenched.

TABLE-US-00003 TABLE 3 composition in weight % Id. Si Fe Cu Mn Mg Cr Ti Zr Extrusion ratio E 1.2 0.11 0.07 0.7 0.8 0.18 0.03 0.04 13 F 1.2 0.12 0.07 0.8 0.8 0.18 0.03 0.04 18.3 G 1.2 0.13 0.08 0.8 0.9 0.19 0.03 0.04 21.8

[0209] The microstructure of the extruded alloys was analyzed using OIM to determine the fractions of main texture components, whereas the Mn containing dispersed particles distribution was characterized using SEM and image analysis techniques.

[0210] SEM experiment were conducted using a number of fields of 294 images with a field size of 53.5 m, which covered a total analyzed surface of 5145 m.sup.2.

[0211] The number density of Mn containing dispersed particles corresponds to the ratio between the total number of Mn containing dispersed particles, which has been identified by the image analysis (by a threshold of grey level set to discriminate aluminum matrix with Mn containing dispersed particles), and the total surface covered by Mn containing dispersed particles.

[0212] The average diameter of Mn containing dispersed particles corresponds to the average Dcircle. The average D.sub.circle corresponds to the equivalent diameter of the circle having the same surface as the average surface over all the Mn containing dispersed particles.

[0213] EBSD measurements were performed at the center of the bar in the L-R plane (L direction corresponding to the extrusion direction and R direction being a radius of the bar). Samples were mechanically polished to 1 m, followed by OPS finishing polishing and an electropolishing with the following conditions (10V 11 s, Kingston solution). The corresponding results of the number density and average diameter or average D.sub.circle of Mn containing particles are given in Table 4.

[0214] EBSD measurements were conducted on a ULTRA55 SEM, HT=20 kV, tilt=70, Working distance=12 mm. The area of investigation was about 2.5 mm (L)1.6 mm (R), with a stepsize of 1.5 m. The acquisition was done at 100 magnification. The data were then analysed using EDAX OIM v7.3.0 software. The grain boundary map assumes a misorientation angle of 15. The fraction of the <001> texture components were determined within 15 deviation around the ideal texture components.

[0215] The EBSD maps were submitted to a clean-up procedure using the Neighbor Orientation Correlation by performing several iterations until the fraction of modified grains is less than 1% and subsequently by applying the Grain dilation level 5 until the fraction of modified grains is less than 1%.

[0216] Results are presented in Table 5.

TABLE-US-00004 TABLE 4 Number of density of Mn containing dispersed particles per m.sup.2 and average Dcircle values. Mn containing Bar Number Dispersed Particles diameter Extrusion density Average Dcircle Id. (mm) ratio (part/m.sup.2) (nm) E Inv. 45 13 3.1 50 F Ref. 60 18.3 2.3 60 G Ref. 55 21.8 1.8 60

[0217] Surprisingly, we observed an effect of extrusion ratio on the number density of Mn containing dispersed particles (degree of concentration of countable Mn containing dispersed particles). The lower the extrusion ratio, the higher the number density. This indicates that the materials extruded at low extrusion ratios tend to exhibit a higher concentration of dispersoids per unit area, which reflects on the Zener drag force as it is proportional to the number density, thus accounting for the higher recrystallization resistance of the extruded forging feedstock with lower extrusion ratio during forging operation. Lowering the extrusion ratio has no effect on the fibrous microstructure, as it can be observed in FIG. 5-7.

[0218] The Table 5 below presents the percentage fraction of texture components corresponding to orientations of the <001> and <111> fiber textures measured in the center of the billet for each extruded bar.

TABLE-US-00005 TABLE 5 Fraction (%) of the texture components of grains with predominant fiber textures <001> and <111>. Extrusion Position: Center of the bar Sample ratio <001> <111> G 21.8 23 74 F 18.3 21 75 E 13 18 73

[0219] It can be first mentioned that the <111> texture is maintained higher than 70% while varying the extrusion ratio. The fibrous microstructure is also retained when decreasing the extrusion ratio, as it is illustrated in FIG. 5 to FIG. 8 where FIG. 5 corresponds to sample G, FIG. 6 to sample F and FIG. 7 to Sample E.

[0220] It is also observed that the lower the extrusion ratio, the lower the fraction of texture components belonging to the <001> fiber. The anti-recrystallization effect due to the Zener drag that prevents recrystallization is further strengthened by limiting the fraction of <001> fiber texture components (e.g. Cube, Goss and rotated Cube) in the feedstock in a content less than 20% by controlling the extrusion ration to less than 15, preferably less than 13. Controlling the fraction of <001> fiber at a maximum of 20% permits to limit the number of potential nuclei for the development of recrystallization textures in the final forged product.