Patent Application
20220389558
The present invention in general relates to aluminum alloy products and, more particularly, such thick products made of alloy 7xxx, their use and manufacturing processes.
In the field of plastics obtained by injection-molding, there is a growing demand for large products. In order to produce molds to manufacture such large products, it is necessary to use thick blocks, i.e. blocks whose thickness is greater than 350 mm, and preferably greater than 450 mm or even greater than 550 mm. “Block” is taken to mean a solid product of essentially parallelepiped shape.
Thick aluminum blocks are also useful in the field of mechanical engineering.
The sought-after characteristics for thick aluminum blocks for the manufacture of molds are high static mechanical properties such as yield strength or ultimate tensile strength, and a high notch strength, these properties being in general antagonistic. Notch strength is an important property for the use of these products and may be characterized for example by the NSR, which is the ratio between the yield strength and strength in the presence of a notch (“Sharp-Notch Strength-to-Yield Strength Ratio”) measured according to standard ASTM E602. For thick products, these properties should in particular be obtained at quarter- and/or mid-thickness and must therefore have low quench sensitivity. It is said that a product is quench sensitive if its static mechanical properties, such as yield strength decreases as the cooling rate decreases. The quenching speed is the average cooling rate of the product during the quench.
Thick blocks should also preferably have low residual stresses. Indeed, the residual stresses cause deformations during machining, which affect the geometry of the mold. Residual stresses can be measured for example by the method described in patent application WO 2004/053180. Low residual stresses typically involve a value WTbar less than 4 kJ/m3, and in general of the order of 2 kJ/m3.
Finally, thick blocks must be obtained by means of a process that is as quick and as economical as possible.
Patent EP1587965 (Alcan) discloses an alloy useful for the manufacture of thick blocks, composed (as a percentage by weight) as follows: 4.6-5.2 Zn; 2.6-3.0% Mg; 0.1-0.2% Cu; 0.05-0.2% Zr; no more than 0.05% Mn; no more than 0.05% Cr; no more than 0.15% Fe; no more than 0.15% Si; no more than 0.10% Ti and a method of manufacturing these blocks, wherein the ingot directly obtained by continuous casting is used as the block.
International application WO 2008/005852 (Alcan) describes an alloy useful for very thick products including (as a percentage by weight) 6 to 8% zinc, 1 to 2% magnesium, dispersoid-forming elements such as Zr, Mn, Cr, Ti and/or Sc.
Alloys of similar composition are also known for other applications. The following are, for example, registered with the Aluminium Association:
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; the rest Al with unavoidable impurities <0.05%, total <0.15%
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; the rest Al with unavoidable impurities <0.05%, total <0.15%
U.S. Pat. No. 3,852,122 (Ardal) discloses an alloy of composition (as a percentage by weight) 4.5-5.8% Zn, 1.0 to 1.8% Mg, 0.10 to 0.30% Zr, 0 to 0.30% Fe, 0 to 0.15% Si, 0-0.25% Mn for making long products used for the manufacture of bumpers, structural parts and also parts used in the manufacture, storage and transport of gases in condensed state.
The patent application FR 2341661 (VMRBA) discloses an alloy of composition (as a percentage by weight) 4.0 to 6.2% Zn, 0.8-3.0% Mg, 0-1.5% Cu, 0.05 to 0.30% Zr, 0 to 0.20% Fe, 0 to 0.15% Si, 0 to 0.25% Mn, 0 to 0.10% Ti to be forged or kneaded by hot working and for use in the construction of vehicles, machines, tanks for appliances and tools.
Patent application JP81144031 (Furukawa) discloses an alloy of composition (as a percentage 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 Cr 0.05-0.20%, for the production of tubes.
The problem to be solved by the present invention is to obtain thick aluminum blocks with an improved balance of properties between static mechanical properties and notch strength, with a low level of residual stresses, by means of a rapid and economical process.
A first object of the invention is an aluminum alloy for the manufacture of thick blocks comprising (as a percentage by weight):
Zn: 5.3-5.9%,
Mg: 0.8-1.8%,
Cu: <0.2%,
Zr: 0.05-0.12%,
Ti<0.15%,
Mn<0.1%,
Cr<0.1%,
Si<0.15%,
Fe<0.20%
impurities with individual content <0.05% each and <0.15% of the total, the remainder being aluminum.
A second object of the invention is a method comprising the steps of:
Yet another object of the invention is a thick block of aluminum obtainable by the process according to the invention characterized in that at ¼ thickness in direction TL, the yield strength RP0.2 and the ratio called NSR between the mechanical strength on a notched test-piece and the yield strength RP0.2 measured according to ASTM E602-03, section 9.2 are such that:
NSR>−0.017*Rp0.2+6.7 and
Rp0.2>320 MPa, preferably 330 MPa
and/or:
NSR>0.8, preferably 1.0.
Yet another object of the invention is the use of a thick block according to the invention for the manufacture of molds for plastics injection-molding.
Unless otherwise stated, all the indications concerning the chemical composition of the alloys are expressed as a percentage by weight based on the total weight of the alloy. The designation of alloys is compliant with the rules of The Aluminum Association (AA), known to experts in the field. The definitions of the tempers are indicated in European standard EN 515.
Unless otherwise stated, the static mechanical properties, in other words, the ultimate elongation at rupture Rm, the tensile yield strength Rp0.2 and elongation at rupture A, are determined by a tensile test according to EN 10002-1 or NF EN ISO 6892-1, the location at which the parts are held and their direction being defined by standard EN 485-1. The mechanical strength on a notched test-piece is obtained in accordance with standard ASTM E602-03. According to standard E602-03, section 9.2, the ratio called NSR between the mechanical strength on a notched test-piece and the yield strength RP0.2 (“Sharp-Notch Strength-to-Yield Strength Ratio”) is calculated, and this ratio gives an indication of the notch strength of the sample.
The problem is solved by an alloy comprising (as a percentage by weight);
Zn: 5.3-5.9%,
Mg: 0.8-1.8%,
Cu: <0.2%,
Zr: 0.05-0.12%,
Ti<0.15%,
Mn<0.1%,
Cr<0.1%,
Si<0.15%,
Fe<0.20%
impurities with individual content <0.05% each and <0.15% of the total, the rest aluminum.
The combination of the zinc content of 5.3 to 5.9% by weight, the magnesium content of 0.8 to 1.8% and the copper content less than 0.2% by weight makes it possible to achieve an improved compromise between mechanical resistance and notch strength. The preferred Zn content is 5.4 to 5.8% by weight. The preferred magnesium content is 1.0 to 1.4% by weight or even 1.1 to 1.3% by weight. The copper content is preferably less than 0.05% by weight or even less than 0.04% by weight.
The zirconium content is 0.05 to 0.12% by weight. Preferably, the zirconium content is at the most 0.10% by weight or even 0.08% by weight, particularly to further reduce the quench sensitivity of the thick aluminum blocks.
The titanium content is less than 0.15% by weight. Advantageously, a quantity 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%. 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 makes it possible to further reduce the quench sensitivity of the thick aluminum blocks.
Si and Fe are unavoidable impurities, the content of which is attempted to minimize, in particular to improve the mechanical strength on a notched bar. The Fe content is lower than 0.20% by weight and preferably lower than 0.15% by weight. The Si content is lower than 0.15% by weight and preferably lower than 0.10% by weight.
A suitable method for making thick alloy blocks according to the invention comprises the steps of
The thick block is preferably cast by semi-continuous direct chill casting. The thick block has a thickness which is greater than 350 mm, and preferably greater than 450 mm or even greater than 550 mm. The block is substantially parallelepiped in shape: it generally has a largest dimension (length), a second largest dimension (width) and a smaller dimension (thickness).
The block may be optionally homogenized, typically by heat treatment at a temperature of between 450 and 550° C. for a period of 10 minutes to 30 hours and/or stress-relieved at a temperature of 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 then undergoes solution heat treatment, i.e. it is heat-treated so that the block temperature reaches 500-560° C. for a time between 10 minutes and 5 hours or even 20 hours. This heat treatment may be performed at a constant temperature or in several steps.
After solution heat treatment, the block is cooled to a temperature below 100° C., preferably to room temperature. Cooling can be performed in still air, with ventilated air, by spraying a mist, by spraying or by immersion in water. Advantageously, the cooling rate is at least 200° C./h.
In a first advantageous embodiment of the invention, the cooling rate is less than 200° C./h. In this embodiment, the residual stresses are low, but the mechanical properties do not reach their maximum values because of some quench sensitivity of the alloy. This cooling rate can be obtained in still air or with a fan.
In a second advantageous embodiment of the invention, the cooling rate is at least equal to 800° C./h. Such a cooling rate can be obtained by sprinkling or immersing in water.
Since too high a cooling rate may generate too great residual stresses in the blocks, water at a temperature of at least 50° C. and preferably at least 70° C. is preferably used for cooling. In this second embodiment the quenched block is stress-relieved, preferably by cold compression with a permanent set of between 1% and 5% and preferably between 2 and 4%. Stress-relieving makes it possible to decrease the residual stresses in the metal and to avoid warpage during machining.
In a third advantageous embodiment of the invention, the cooling rate ranges between 200° C./h and 400° C./h. Surprisingly, when the cooling rate lies between 200° C./h and 400° C./h, satisfactory mechanical characteristics and low residual energy can simultaneously obtained making it possible to do away with the stage of stress-relieving by compression. Such a cooling speed can be obtained by fine spraying.
Finally, the solution heat treated and cooled block is tempered. Tempering is performed so that the block reaches a temperature of 120 to 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, tempering is performed to reach temper T6 or T652, corresponding to the peak of the static mechanical properties (Rm and Rp0.2).
Between each operation, it is possible to perform simple operations of sawing the block and/or machining its surfaces.
However, said block is not subjected to any significant deformation by working between casting and tempering. “Working” is typically taken to mean hot rolling or forging operations. “Significant deformation” means that none of the dimensions of the cast block—which is a thick block, substantially parallelepiped in shape (length L, width TL, thickness TC)—undergoes significant change, i.e. typically of at least about 10%, by working between the casting and the tempering. In other words, none of the dimensions of the cast block undergoes a relative change as a result of working of typically more than 10% as an absolute value, which means that said working causes no permanent deformation in each direction L, TL, TC greater than a value close to Ln(1.1)=0.095 and corresponds to a generalized plastic deformation
typically less than 0.135.
The thick blocks obtained by the method according to the invention have an advantageous compromise of properties, in particular between the yield strength and notch strength which are two antagonistic properties (the higher the one, the lower the other). More specifically, the applicant found that for a thick block of an alloy having the composition according to the invention, obtained by following the steps claimed in the process as far as the tempering stage (casting, optional homogenization and stress-relieving, solution hardening and quenching without any significant working between casting and the final tempering stage), regardless of the tempering treatment (single or multi-stage) then performed to achieve a given yield strength Rp0.2, the NSR (“Sharp-Notch Strength-to-Yield Strength Ratio”), i;e. the parameter used to characterize the notch strength of the block thus obtained, reaches a value which does not depend on the annealing treatment performed to obtain the targeted Rp02. We can therefore establish for such thick blocks a relationship between the measured Rp02 and NSR e.g. at ¼ thickness, and this relationship appears to be substantially linear.
The applicant has therefore been able to establish that, when the method of the first embodiment is used, notch strength as assessed at ¼ thickness in direction TL by the NSR (the ratio measured according to ASTM E602-03, section 9.2) is greater than:
−0.017*Rp0.2+6.4.
Typically, the NSR is at least 0.7, preferably 0.8 and the yield strength is at least 320 MPa, preferably 330 MPa.
When the method of the second embodiment is used, notch strength as assessed at ¼ thickness in direction TL by the NSR (the ratio measured according to ASTM E602-03, section 9.2) is greater than:
−0.017*Rp0.2+6.7.
Typically, the NSR is at least 0.8, preferably 1.0 and the yield strength is at least 320 MPa, preferably 330 MPa.
Simultaneously obtaining high mechanical strength and high notch strength is a surprising result.
The thick blocks of the invention are advantageously used to manufacture molds for injection-molding plastics.
The examples of the invention are referred to as A and B. Examples C, and D are presented for purposes of comparison. The chemical compositions of the various alloys tested in this example are given in table 1.
Alloys A, B, C and D were cast in the form of blocks of thickness 625 mm.
Alloy blocks A and C were processed as follows: the blocks were first homogenized for 10 h at 480° C. The blocks were then solution heat treated for 4 hours at 540° C. and air cooled to about 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 subjected to tempering, first at 105° C. for about 12 hours and then at 160° C. for about 16 h.
Alloy blocks B and D were processed as follows: the blocks first underwent stress-relieving for 2 hours at 350° C. After solution heat treatment for 4 h at 540° C. (block B) or 10 h at 475° C. (block D), the blocks were cooled with water at 80° C. by immersion. The blocks were then subjected to stress relieving by compression of 3%. The alloy B blocks were then subjected to tempering of 130° C. for 24 h (block B1) or 150° C. for 16 h (block B2). The alloy D block meanwhile underwent tempering treatment first at 90° C. for 8-12 h and then at 160° C. for 14-16 h.
The mechanical properties obtained, measured at ¼ thickness in the direction TL are presented in Table 2
Under identical transformation conditions, alloy A according to the invention provides, when compared to alloy C, a simultaneous improvement in the yield strength and the NSR ratio, and therefore in notch strength. The NSR ratio obtained is greater than
−0.017*Rp0.2+6.4.
The preferred transformation process of the alloy according to the invention can further improve the NSR ratio. The block B alloy of the invention achieved an NSR ratio greater than
−0.017*Rp0.2+6.7.
This ratio is not attained by alloy D in similar transformation conditions.
| Number | Date | Country | Kind |
|---|---|---|---|
| 1004865 | Dec 2010 | FR | national |
This application is a Divisional of U.S. application Ser. No. 13/994,097, filed Jun. 13, 2013, which is a § 371 National Stage Application of PCT/FR2011/000637, filed Dec. 6, 2011, which claims priority to French Application No. 10/04865, filed Dec. 14, 2010. Each of these applications is incorporated by reference in its entirety.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 13994097 | Jun 2013 | US |
| Child | 17678591 | US |
