A1 alloy and method

Details A1 alloy and method A1 alloy and method

1999-07-08

2003-04-08

Wyszomierski, George (Department: 1742)

Metal treatment

Stock

Aluminum base

C148S692000, C420S544000, C420S547000

Reexamination Certificate

active

06544358

ABSTRACT:

This invention is concerned with a new alloy in the 5000 Series of the Aluminum Association Register. Ingots of the alloy can be converted to rolled sheet which can be formed into shaped components for use in vehicles.
Non-heat-treatable alloys of the Al—Mg (5xxx) type are well suited to the application of automotive structural pressings to form a body-in-white structure. In the soft annealed condition (O-temper) these alloys can have high formability allowing the complex structure pressings to be manufactured. Subsequent heat treatment during the car manufacture (e.g. paint-bake ovens) reduces the as deformed strength back close to the O-Temper properties due to thermal recovery. Unlike heat-treatable alloys, these properties are then stable throughout the life of the vehicle, i.e. no artificial ageing takes place.
The alloy AA5754 is a well known non-heat-treatable 5xxx series alloy, (2.6 to 3.6% wt Mg). The specification, given in Table 1, is broad and as such far too wide for the automotive industry. The Mg level must be controlled to tighter limits to maintain an acceptable spread of proof stress values in the final sheet. Also, to render the alloy sufficiently formable, it is usually based upon low Si and Fe (about 0.08% wt Si and about 0.2% wt Fe) requiring virgin smelter metal. Such alloys are not readily recyclable because during each remelting the Si and Fe levels increase and quickly exceed the level at which formability declines. There is a need for an alloy that can be recycled. This is particularly true of alloys intended for use in the mass production of automobiles. Alloys which require smelter metal obviously are not recyclable.
TABLE 1
AA5754
Si
Fe
Cu
Mn
Mg
Cr
Zn
Ti
AA 5754
Max
0.40
0.40
0.10
0.50
3.6
0.30
0.20
0.15
Limits
Min
2.6
Conventional 5xxx series structural alloys have either lower strength, due to a reduced Mg and Mn level (such as AA5251 and AA5754), or have equivalent/greater strength but are sensitive to intergranular corrosion and Stress Corrosion Cracking (such as AA5182).
This invention relates to the development of an alloy composition and processing route which gives rise to a higher strength 5xxx series alloy which is insensitive to SCC, and tolerant to high levels of Si and Fe in terms of formability. A characteristic of the current alloy is that because it can contain high levels of Si and Fe, it is therefore more recyclable.
In one aspect the present invention provides an alloy of composition in wt %:
Si 0.10-0.25 preferably 0.10-0.20
Fe 0.18-0.30 preferably 0.20-0.30
Cu up to 0.5 preferably up to 0.3
Mn 0.4-0.7 preferably 0.4-0.5
Mg 3.0-3.5
Cr up to 0.2 preferably up to 0.1
Ti up to 0.1
Others up to 0.05 each, 0.15 total
Al balance
This is a relatively high-strength alloy, it has a 0.2% proof strength of 105-110 MPa, compared to 90-95 MPa for the standard AA5754 alloy containing 2.9 wt % Mg.
Components for load bearing structures in automobiles are press formed which involves stretch forming and deep drawing Deep drawing is often the most important process, and this calls for a high r value, that is to say a high plastic strain ratio, that is uniform in the plane of the sheet. This need is met by the alloys of the invention.
Mg is the principal solid solution strengthening addition in the alloy. The Mg content of the alloys of this invention, which is relatively high at 3.0-3.5%, results in increased strength and formability. However, if the Mg level is raised too far, then intergranular corrosion and stress corrosion cracking (SCC) problems, associated with the formation of an Al
8
Mg
5
precipitate at grain boundaries, restrict performance. For batch annealed material, an upper limit of Mg is set at 3.3%. For continuously annealed and solution heat-treated (CASH) material, the Mg content may be pushed up as high as 3.5%.
Mn is present at relatively high levels of 0.4-0.7% preferably up to 0.6% more preferably up to 0.5%. Homogenisation of the alloy results in precipitation of &agr;-AlMnSiFe particles which give rise to additional dispersoid strengthening. Very high Mn levels are detrimental due to the formation of a coarse intermetallic phase MnAl
6
. The increased density of dispersoids causes a refinement of the O temper grain size and a resultant increase in strength.
Cu may be present at levels up to 0.5% preferably up to 0.3%, more preferably up to 0.10%. At higher levels (e.g. up to 0.3%), Cu gives rise to significant strength retention after a paint bake cycle. Above 0.3% no additional benefit is obtained. Cu is an inevitable impurity in recycled scrap. Cu levels above 0.15% give rise to alloys having high r values but which may (unless the working conditions are rather closely controlled) be detrimental by virtue of very pronounced variation in the plane of the sheet (high &Dgr;r).
Si is present at 0.10-0.25% preferably up to 0.20% and improves strength. High Si and Mn have surprisingly been found to improve the r value of sheet and to promote uniformity in the plane of the sheet (low &Dgr;r). But Si content as high as 0.3% gives rise to reduced ductility and reduced formability.
Fe is specified at 0.18-0.30% preferably 0.20-0.30%. Fe contributes to dispersion strengthening, but at high concentrations lowers formability.
The Si and Fe levels are set such that the alloy can be produced from recycled metal. Recycling increases the Si and the Fe levels in the charge. It also increases the Cu content. The new alloy of the invention is more tolerant of these impurities.
Cr has similar effects to Mn and may be used in partial replacement of Mn. Preferably the (Cr+Mn) content is at least 0.4%. Preferably Cr is not deliberately added to the alloy, i.e. is present only as an incidental impurity at up to 0.05%.
Ti may be added to refine the grain structure.
Other alloying components may be present in minor concentrations up to 0.05% each, 0.15% total. Components deliberately added may include Zn and B. Other components would normally be present only as adventitious impurities. The balance of the alloy is Al.
In another aspect the invention provides rolled and annealed sheet of the alloy described. (Rolled sheet for canstock is used in a hard as-rolled condition). The following paragraphs describe the processing steps used to produce that rolled sheet.
Molten metal of the required composition is cast, typically by direct chill casting although the casting technique is not material to the invention. An ingot of the alloy is homogenised, preferably at a relatively high temperature of at least 500° C. preferably 530-5800° C. particularly 550-580° C., for 1-24 hours. Homogenisation is preferably performed under conditions that result in the formation of a fine dispersoid of &agr;-AlMnSiFe particles. If the homogenisation temperature is too low, it is possible that this may be produced as a coarser needle-like precipitate which exhibits growth with increased homogenisation time. These needles can break up during rolling to create voiding in the structure, resulting in possible reduced ductility. Homogenisation at sufficiently high temperature results in spherical precipitates being formed which do not break up during rolling. These dispersoids are also relatively stable in size with homogenisation times up to 16 hours and possibly beyond.
The homogenised ingot is then hot rolled and cold rolled, both under conditions which may be conventional. During cold rolling, an interanneal is optional, preferably at a temperature of 300-400° C. in batch operation or at 400-550° C. in continuous operation. When an interanneal is employed, a final cold rolling treatment results in a thickness reduction preferably in the range 40-60% e.g. about 50%. A final annealing step, preferably at 300-400° C. for 0.05-5 hours in batch operation, or at 400-550° C. in continuous operation, may be carried out on a batch basis, or as a continuous anneal and solution heat treatment. Annealing conditions should be such as result in a fully recrystallised grain structure i.e. one produced by high angle grain boundaries sweeping through the structure. Such alloys have

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