CN101384741A - Aluminium alloy with improved crush properties - Google Patents
Aluminium alloy with improved crush properties Download PDFInfo
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- CN101384741A CN101384741A CNA2007800058797A CN200780005879A CN101384741A CN 101384741 A CN101384741 A CN 101384741A CN A2007800058797 A CNA2007800058797 A CN A2007800058797A CN 200780005879 A CN200780005879 A CN 200780005879A CN 101384741 A CN101384741 A CN 101384741A
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- 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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- 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
Abstract
An Al-Mg-Si alloy with improved ductility and crush properties, in particular useful for structural components in crash exposed areas in vehicles. The alloy contains in wt %: Mg 0,25 - 1,2; Si 0,3 - 1,4; Ti 0,03 - 0,4, where Ti is present in solid solution and where the alloy contains in addition one or more of the following alloy components: Mn max 0.6; Cr max 0.3; Zr max 0,25, and incidental impurities, including Fe and Zn up to 0,5 with balance Al.
Description
Technical field
The present invention relates to have the Al-Mg-Si aluminium alloy of the ductility and pressure break (crush) performance of improvement, this aluminium alloy has good energy absorption and temperature stability, and is specially adapted to the structure unit in the vehicle collision exposed region.
Background technology
US 4 525 326 discloses a kind of Al-Mg-Si alloy, adds vanadium V to improve alloy ductility.Describe in this patent, add 0.05-0.20 weight %V and, significantly improved the ductility of the Al-Mg-Si alloy of wide region in conjunction with the Mn content that is defined as Fe content 1/4-2/3.In US 4 525 326, do not mention titanium Ti, and (US 5 766 546 in identical contriver's the patent of concrete grammar subsequently, EP 1 104 815) in also not mentioned titanium Ti, wherein used by adding V and improving the principle of ductility in conjunction with Mn and other element.
In EP 0 936 278, described by add 0.05-0.20 weight %V and in conjunction with adding 0.15-0.4 weight %Mn improves the ductility of Al-Mg-Si alloy.According to this european patent application, preferred L n/Fe is than being 0.45-1.0, more preferably 0.67-1.0.The effect that offers some clarification on Ti in EP 0 936278 is as grain-refining agent in casting or welding process.Yet the preferable range of Ti is no more than 0.1 weight %.
Adding Ti in ceralumin is known for producing Al-Si base casting alloy.Therefore, the previous Ti that surpasses Ti known Ti amount in grain-refining agent is used by adding of confirming, the grain refining that is improved for these alloys, as at C.J.Simensen:Proc.LightMetals 1999, ed.C.E.Eckert, TMS describes among USA 1999 pp679-684.The benefit of adding excessive Ti relates to grain refining, and relates to performance relevant with grain-size in the casting metal.Yet it is favourable to the performance beyond the grain-size correlated performance not confirm to add excessive Ti.
Summary of the invention
The present invention relates to contain the aluminium alloy of Mg and the main alloy element of Si conduct.The Ti that alloy according to the present invention contains surpasses the Ti that adds as grain-refining agent usually.The Ti that alloy of the present invention contains surpasses by what grain-refining agent was introduced and contains the Ti particle.Excessive Ti helps to improve the ductility of alloy.
This alloy can contain Cu in order to obtain extra intensity.In addition, this alloy can contain Fe and Zn and deposits impurity as idol.In addition, this alloy can contain other alloy element, includes but not limited to that Mn, Cr, Zr and V are in order to the further ductility of improving alloy.
Develop the squeezing prod that this alloy is used for the good pressure break behavior of needs.For productivity is optimized this alloy and be need not in extrusion machine extruded section (profile) to be carried out rapid quenching in order to the ductility that obtains.Yet when ductility that needs improve, alloy also can be used for other products for example rolled sheet or forging.
The invention is characterized in the feature that appended independent claim 1 and dependent claims 2-8 limit.
Description of drawings
To and further describe the present invention with reference to the accompanying drawings by embodiment below, wherein:
Fig. 1 shows aluminum alloy extrusion section bar with various Mg and the Si content coordinate diagram at the percentage of total elongation of age hardening after the highest hardness,
Fig. 2 has shown the cross-sectional geometry of the extruded hollow section bar that is used for the test of specification sheets embodiment pressure break,
Fig. 3 has shown the yield strength and the grade in the pressure break test of the sample of specification sheets embodiment 1,
Fig. 4 has shown owing to expose 1000h 150 ℃ of heat, the yield strength (YS) of the age hardening extruded section of the ALLOY O of specification sheets embodiment 2 and P and the reduction of ultimate tensile strength (UTS),
Fig. 5 has shown alloy in the specification sheets table 4 at 175 ℃ with in the variation with the timeliness time of 200 ℃ Vickers' hardness,
Fig. 6 has shown recrystallize 6005A alloy and non-recrystallize 6082 alloys at T5 state and the tensile yield strength after high temperature exposure,
Fig. 7 has shown the yield strength and the grade in the pressure break test of the sample of specification sheets embodiment 3,
Fig. 8 has shown the yield strength and the summer specific energy of and age hardening sample cold according to the shrend of specification sheets embodiment 4,
The grade of the sample that Fig. 9 has shown specification sheets embodiment 4 in the pressure break test, shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing,
Figure 10 has shown two photos, left photo has shown the grain structure of the alloy variant B1 with 0.15%Mn and 0.1%V, and right photograph has shown that the element of finding has the grain structure of the alloy variant B3 of 0.06%Cr in addition in the alloy B 1 of embodiment 4
The grade of the sample that Figure 11 has shown embodiment 6 in the pressure break test is squeezed into geometrical shape P3 with velocity of discharge 15m/min, and wherein shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing,
It is identical with Figure 11 that Figure 12 shows, but wherein velocity of discharge is 30m/min, and comprising the yield strength of sample,
Figure 13 has shown the yield strength and the grade in the pressure break test of the sample of specification sheets embodiment 7, described sample is squeezed into geometrical shape P1 with velocity of discharge 15m/min, it is cold to carry out shrend then before age hardening, wherein shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing
Figure 14 has shown the grade of sample in the pressure break test of specification sheets embodiment 7, described sample is squeezed into geometrical shape P1 with velocity of discharge 15m/min, advance line space air cooling but in age hardening then, wherein shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing
Figure 15 has shown the grade of sample in the pressure break test of specification sheets embodiment 7, described sample is squeezed into geometrical shape P3 with velocity of discharge 15m/min, advance line space air cooling but in age hardening then, wherein shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing
Figure 16 has shown the yield strength and the grade in the pressure break test of the sample of specification sheets embodiment 7, described sample is squeezed into geometrical shape P3 with velocity of discharge 30m/min, advance line space air cooling but in age hardening then, wherein shown the nominal content of Mn, V, Cr, Cu and the Ti of different-alloy in drawing
Figure 17 has shown the relation of the summer specific energy and the pressure break test middle grade of embodiment 6 samples, and described sample is squeezed into geometrical shape P3 with velocity of discharge 30m/min, and advances line space air cooling but in age hardening,
Figure 18 has shown the yield strength between the respective alloy of the alloy of table 9 and table 8 and the difference of summer specific energy, and wherein all samples all are squeezed into geometrical shape P3 with velocity of discharge 30m/min, and advance line space air cooling but in age hardening,
Figure 19 shown when the yield strength and the summer specific energy that section bar are carried out shrend specification sheets table 10 alloy when cold before age hardening,
Figure 20 has shown the yield strength and the summer specific energy of table 10 alloy when before age hardening section bar being carried out air cooling,
Figure 21 has shown the Mg-Si phasor, wherein draws 1.4 Si/Mg ratio, and as the concrete alloy composition of paying close attention to of the embodiment of the present invention defined in the claim.
Embodiment
Al-Mg-Si type alloy obtains their intensity by the particle of separating out nano-scale.As known, described hardened granules has about 1 Si/Mg mol ratio (people such as G.A.Edwards, Mater.Sci.Forum 217-222 rolls up (1996) 713-718 page or leaf), some studies show that this ratio accurately is 1.2 (people such as S.J.Andersen, Acta Mater. the 49th volume (1998) 65-75 pages or leaves, C.Ravi and C.Wolverton, Acta mater. the 52nd volume (2004) 4213-4227 pages or leaves).1.2 the Si/Mg mol ratio corresponding to 1.4 Si/Mg weight ratio, therefore, hereinafter, the Si/Mg ratio that all provide all refers to weight ratio.In order to optimize the intensity of alloy, should select Mg and Si content to form the sclerosis precipitate to guarantee to use Mg as much as possible and Si, or in other words the least possible to guarantee after precipitation-hardening remaining Mg or Si.For residue Mg or Si, be interpreted as not forming the Mg or the Si of precipitate.Residue Mg or Si almost do not contribute for intensity, but the productivity in the extruding is had remarkable negative impact.The method of the Mg of this selection extruded alloy and Si content before was utilized (U.Tundal and O.Reiso, United States Patent (USP) 6,602,364, people Proc.Eighth International Aluminum Extrusion Technology Seminar such as M.J.Couper, Orlando Florida, USA, in May, 2004,18-21 day II rolled up the 51-56 page or leaf), and it is well-known to be considered to those skilled in the art.
In order to find the best Si/Mg ratio of alloy, people must consider that some Si can be bound in other the non-hardened granules that contains the Fe primary particle and form in alloy casting and homogenizing process.Can think this Si " loss " or for not effect of age hardening.Those skilled in the art can introduce by the term of following formula definition " effectively Si content ", Si
Eff:
Si
eff＝Si
tot-Si
nhp
Si wherein
TotBe total Si content of alloy, Si
NhpIt is the Si amount that is strapped in the non-hardened granules.Can not directly calculate Si
Nhp, because this not only relates to alloy composition but also relates to thermal history in the homogenizing process.Yet, find ratio usually
Si
NhpThe scope of [weight %]/(Fe+Mn+Cr) [weight %] is 0.15-0.35.
Therefore, Si
Eff/ Mg ratio should be 1.4 so that optimize alloy strength.
Form for the Mg of pressure break ductility and temperature stability and the optimization of Si
The extruded section that uses the Al-Mg-Si alloy is as the structure unit in the car collision exposed region.Require such parts to absorb big energy when collision, they must be out of shape and not break for this reason.It is a kind of that to control the mode that extruded section has desired properties be by axial pressure break it to be tested.In this test, make the thin-walled extruded section sample of predetermined length, be generally hollow material with one or more chambeies, be out of shape in a longitudinal direction with controlled speed, this reduces to specimen length the 30-80% that is generally initial length.Good deformational behavior be characterised in that the sample wall regular fold, have and almost do not have or do not have the sample cracking and deformed region has smooth surface.The deformational behavior of difference is characterised in that limited fold, the sample of sample wall have a large amount of crackings or breaks and deformed region has coarse and uneven surface.
Axially the deformational behavior in the pressure break test depends on the geometrical shape of test section bar strongly and depends on test condition to a certain extent.For geometrical shape, the cross section particularly important of section bar.One concerns it is that good deformational behavior is difficulty gradually when the wall thickness increase with when the chamber size reduces usually.Except that the geometrical shape and test condition of test section bar, also there are several factors that in the pressure break test, influence deformational behavior, include but not limited to grain structure, intensity and the ductility of extruded section.Intensity is mainly by Mg and Si (and Cu) content and the precipitation-hardening conditional decision selected.Usually, higher Mg and Si (and Cu) content and higher-strength therefore cause lower ductility, are for example found by as shown in Figure 1 the percentage of total elongation value in the tension test, therefore also cause relatively poor behavior in the pressure break test.Yet the Si/Mg ratio has certain importance for the pressure break behavior of extruded section.This is confirmed by the following examples.In all embodiments, the DC castingprocesses that uses in the production unit by the applicant becomes briquet with alloy casting.Briquet carries out homogenizing under 570-580 ℃ of temperature, subsequently with 300-400 ℃/hour speed cool to room temperature.Before extruding, in induction furnace, briquet is heated in advance 490-500 ℃ temperature.
The alloy that following table 1 provides is tested, and these alloys have essentially identical composition except that the Si/Mg ratio.By these alloy extruded hollow section bars, cross section as Fig. 2 a) shown in.Compression ratio is 24 in extrusion process, and the section bar velocity of discharge is 15m/min.Section bar carries out shrend in extrusion machine cold, and timeliness is to highest hardness and cut into the long sample of 100mm.In controlled axial pressure break, sample is compressed to 40mm length, thereby and characterizes the grade that deformational behavior provides scope 1-10.
Provide the definition of different grades in the table 2.Three samples of every kind of alloy are carried out pressure break so that opinion rating, and the grade of alloy is the arithmetical av of three samples.Fig. 3 has shown the grade of each alloy as the Si/Mg proportion function.Fig. 3 has also shown the yield strength of different-alloy.
The composition of table 1 embodiment 1 alloy
| Alloy | Mg | Si | Si/Mg | Fe | Mn | V | Ti |
| A1 | 0.35 | 0.66 | 1.89 | 0.20 | 0.15 | 0.10 | 0.01 |
| B1 | 0.39 | 0.57 | 1.46 | 0.20 | 0.15 | 0.08 | 0.01 |
| C1 | 0.44 | 0.54 | 1.23 | 0.21 | 0.14 | 0.09 | 0.01 |
| D1 | 0.50 | 0.47 | 0.94 | 0.20 | 0.16 | 0.09 | 0.01 |
| E1 | 0.52 | 0.44 | 0.85 | 0.20 | 0.15 | 0.10 | 0.01 |
| F1 | 0.58 | 0.42 | 0.72 | 0.22 | 0.15 | 0.09 | 0.01 |
The grade explanation of table 2 pressure break test sample
| | Explanation | |
| 10 | No orange peel, flawless | |
| 9 | Some orange peels, a |
|
| 8 | Orange peel clearly, some |
|
| 7 | Serious orange peel, some |
|
| 6 | Shallow horizontal crackle, some |
|
| 5 | Darker horizontal crackle, |
|
| 4 | Dark horizontal crackle, |
|
| 3 | The horizontal crackle that runs through wall, some |
|
| 2 | The horizontal crackle that runs through wall, serious broken | |
| 1 | Whole fragmentation |
Although all alloys all demonstrate good behavior in pressure break test, however the slightly inferior properties of alloy A 1 with the highest Si/Mg ratio in other alloy, and the Si/Mg ratio very the alloy B 1 near ideal value 1.4 is better than the slight summary of performance with other alloy phase.Alloy C1, D1, E1 and F1 all obtain grade 9 in this test.When considering the intensity of alloy, it is better than performance with the alloy phase with higher-strength in this test to wish to have more low intensive alloy.Therefore, consider intensity, can think in alloy C1, D1, E1 and F1, when Si/Mg ratio improved performance the pressure break test when 0.7 is increased to 1.2.Therefore, for the pressure break test performance, selection Si/Mg ratio is favourable near 1.4 alloy.
Some structure units in the collision exposed region also may be exposed to the temperature of rising.Such exposure may influence the mechanical property of alloy.Use for these, importantly select less being heated to expose the alloy of influence.Term " thermostability " refers to alloy keeps mechanical property after high temperature exposure ability.For the Al-Mg-Si alloy, find in given strength grade, the highest for the alloy thermostability of Si/Mg ratio about 1.4.This is confirmed by the following examples.
Embodiment 2.1
The Al-Mg-Si alloy that following table 3 provides is tested, and these alloys are basic identical except that the Si/Mg ratio.Three kinds of different slightly ageing treatment that by applying marking are I, II and III are carried out age hardening to the extruded section of these alloys.The sample of age hardening is at 150 ℃ of hot down 1000h that expose then.In table 3, provide the yield strength (YS) and the ultimate tensile strength (UTS) that obtain by ageing treatment I, II and III, and in Fig. 4, shown the Strength Changes that hot exposure causes.
The chemical constitution of table 3 embodiment 2.1 alloys and the yield strength (YS) and the ultimate tensile strength (UTS) that cause by different ageing treatment I, II and III.
Apparent by test result shown in Figure 4, be that 0.9 ALLOY O is compared with the Si/Mg ratio, the Si/Mg ratio is that 1.4 alloy P has lower loss of strength, particularly ultimate tensile strength.Therefore can think and have high thermal stability at these two kinds of alloy interalloy P.
Embodiment 2.2
The alloy that following table 4 provides is further tested.Except that the Si/Mg ratio, the alloy of table 4 is basic identical.To the extruded section sample of these alloys at 175 ℃ and 200 ℃ of following artificial aging 0.5h-200h.Measure the Vickers' hardness of sample, and the result as shown in Figure 5.For clear, only show result near highest hardness.It is evident that from the curve of Fig. 5 in the alloy of table 4, alloy W2 has near peaked hardness in the wideest time span.Find as one man that also the hardness reduction (be called overaging) of alloy W2 after reaching peak hardness more lags behind than other alloy.Fig. 5 also shows when the Si/Mg ratio is departed from gradually by ideal value 1.4, for example from alloy W3 to W4 then to W5, overaging have a hysteresis that shortens gradually.Can think that the alloy that carries out longer aging time before overaging takes place has higher thermostability, so the Si/Mg ratio has the highest thermostability near 1.4 alloy.
The composition of table 4: embodiment 2.2 alloys
| Alloy | Si | Mg | Si/Mg | Fe[wt.％] | Mn[wt.％] |
| W1 | 0.81 | 0.48 | 1.69 | 0.21 | 0.020 |
| W2 | 0.78 | 0.51 | 1.52 | 0.19 | 0.016 |
| W3 | 0.72 | 0.56 | 1.29 | 0.20 | 0.016 |
| W4 | 0.65 | 0.60 | 1.08 | 0.21 | 0.017 |
| W5 | 0.59 | 0.71 | 0.84 | 0.20 | 0.015 |
Embodiment 2.3
The alloy of recrystallize and non-recrystallize is tested in addition to observe the influence of grain structure to thermostability.The 6005A of use in embodiment 2.3 and the composition of 6082 alloys in following table 5, have been provided.In both cases, carry out extruded section, and it is cold to carry out shrend after extruding with 15m/min.The Mn content of alloy 6005A is too low so that can not stop the recrystallize of material in the extrusion process, thereby has the grain structure of recrystallize.On the other hand, therefore 6082 alloys have the grain structure of non-recrystallize because high Mn and Cr content contains a large amount of dispersoid particles.
The composition [weight %] of table 5 embodiment 2.3 alloys
| Alloy | Si | Mg | Fe | | Mn | Cr | |
| 6005A | 0.60 | 0.55 | 0.20 | 0.15 | 0.16 | - | |
| 6082 | 0.91 | 0.63 | 0.17 | - | 0.56 | 0.15 |
With the material timeliness of two kinds of alloys to T5 state, referring to Fig. 6 near maximum potential strength.By subsequently when carrying out high temperature exposure for 180 ℃, the 6005A alloy material demonstrates more stable than 6082 alloy materials.The major cause most probable of this species diversity is relevant with the grain structure difference of extruded material.The grain structure of non-recrystallize will have more multidigit mistake and subgrain boundary, and this can serve as the rapid diffusion passage of alloy element.Therefore, sclerosis Mg-Si precipitate will be than in the recrystallize 6005A alloy alligatoring taking place quickly in 6082 alloys of non-recrystallize.
Extruding postcooling speed is to the influence of behavior in the pressure break test
For the Al-Mg-Si alloy, find that usually ductility after the age hardening depends on the rate of cooling after carrying out solution heat treatment.Al-Mg-Si alloy for extruding do not use independent solution heat treatment usually, so the ductility after the age hardening depends on the rate of cooling of section bar in extrusion machine.High rate of cooling (for example using the cold acquisition of shrend) helps good ductility, and slow rate of cooling (for example using air cooling to obtain) can cause the ductility that reduces.
Ideally, after extruding section bar should to carry out shrend all the time cold.Yet, the cold distortion that causes the crimping section geometrical shape of shrend, and along with the complicacy of section bar increases, distored risk increases.Usually way is should cool off as quickly as possible and do not cause the distortion of section bar geometrical shape.Therefore, use forced ventilation or use controlled water spray that main crimping section is cooled off.
After extruding because the ductility of the reduction that the rate of cooling that reduces causes also will have strong influence to the performance that pressure break is tested interalloy.Show among this embodiment 3 below.
Consider the alloy of table 1.Carry out the test identical, just this time use the extruding back in forced ventilation, to carry out the refrigerative section bar with embodiment 1.Cooling time between 500-250 ℃ is according to being measured as about 2 minutes.Carry out axial pressure break test, provide grade according to last table 2.Fig. 7 has shown the grade and the yield strength of each alloy.
For the cold sample of the shrend of same alloy, grade is 8.5-9.5 (Fig. 3), and in this embodiment, grade is in the 5-6 scope.This clearlys show that rate of cooling after the extruding is to the influence of alloy pressure break behavior.
Again, should according to these alloys than low strength, the grade of alloy D1, E1 and F1.In the overall evaluation, think that alloy C1 has best pressure break behavior in this embodiment.
The pressure break behavior of embodiment 3 significantly is worse than embodiment 1, and shrend is cold will to limit section bar geometrical shape and the geometric tolerances that can supply but use as embodiment 1.Therefore inventor's decision is sought to have near the pressure break behavior of embodiment 1 but can carry out air cooled alloy after extruding.Those skilled in the art is known, adds the ductility that element M n, Cr and V can improve the air cooling extrusion of Al-Mg-Si alloy on a small quantity.
Improve the alloy element of extruding Al-Mg-Si alloy ductility.
Manganese (Mn) and chromium (Cr) have several known effects in the Al-Mg-Si extruded alloy.These two kinds of elements all form small-particle in the homogenizing process of cast material, these small-particles are called as dispersoid.When existing with enough number densitys, these dispersoids can stop the extruded material recrystallize, cause fibrous microstructure.For the dispersoid of low number density, extruded material is recrystallize, but the existence of dispersoid has favourable influence to the ductility of age hardening material.Have been found that this influence part is relevant with the texture of material.For the alloy of recrystallize after extruding, in extruded section, find the cubic texture of height usually.The existence of dispersoid causes having the cubic texture of higher degree in the extruded section of recrystallize.
The alloy that following table 6 provides is tested, and these alloys are basic identical except that Mn and Cr content.
The composition of table 6: embodiment 4 alloys
| Alloy | Mg | Si | Fe | Mn | Cr |
| T1 | 0.48 | 0.69 | 0.23 | - | - |
| T2 | 0.48 | 0.69 | 0.23 | 0.16 | - |
| T3 | 0.48 | 0.69 | 0.23 | 0.16 | 0.07 |
These alloys are squeezed into flat excellent section bar.This produces the cubic texture of height in alloy material.Some materials are carried out additional hot mechanical treatment to facilitate the material that does not have texture as far as possible.In table 7, provided the texture intensity that obtains.
Table 7: the texture intensity of measuring in the sample
| Sample | Texture intensity [* random] |
| T1 is random | 4 |
| |
26 |
| T2 is random | 3 |
| T2 cube | 31 |
| T3 is random | 3 |
| |
34 |
Sample is carried out solution heat treatment, and the cold or air cooling of shrend is to room temperature.Subsequently sample is labeled as in this embodiment 5 kinds of different ag(e)ing processes of a1-a5.Material to age hardening carries out Elongation test and Xia Bi test, and the result of the cold sample of shrend shown in Figure 8.By comparison diagram 8a), c) and e), they all derive from untextured material, find that Mn and Cr have positive effect to ductility.Yet, when untextured material and cubic texture material being compared (Fig. 8 a) and 8b), 8c) and 8d) and 8e) and 8f)) time, can know the summer than test in cubic texture have significant positive effect for the ductility of alloy.Also find similar result for air cooled sample before age hardening.For Cr, the amount of the dispersoid that the interpolation element of every weight percent forms is significantly higher than Mn (O.Lohne and A.L.Dons:Scand.J.Metall. the 12nd volume, (1983), the 34-36 page or leaf), this means with respect to Mn and add, need less Cr to add the dispersoid that can obtain certain number density.Dispersoid has three kinds of detrimental actions for extrusion process.First kind of thermal deformation resistant raising that detrimental action is a material causes the productivity potentiality to reduce.Second kind of detrimental action is that the dispersoid density that increases makes that the raising to rate of cooling requires to avoid losing the sclerosis potentiality of alloy after extruding.Reason about this is that dispersoid serves as the nucleation site of non-sclerosis Mg-Si precipitate.The third detrimental action is relevant with the grain-size of extruded section.If the number density of dispersoid is too low so that can not stop recrystallize, but its still to stop some nucleus growths be recrystal grain.Owing to only have a small amount of crystal grain to grow, the possibility of result is to have very thick grain structure in extruded section.When forming extruded section subsequently, the possibility of result is that significant orange peel produces.Therefore attempt to avoid Mn and Cr addition to surpass and improve the necessary addition of ductility.The optimum content of Mn and Cr depends on the geometrical shape of treatment condition and section bar strongly.For many conditions, the addition that typically improves ductility is 0.03-0.25 weight %Mn and 0.01-0.15 weight %Cr.If with these two kinds of element combinations, may need to reduce the amount of every kind of element to keep the dispersoid sum in acceptable level.
Zirconium (Zr) also is the alloy element that forms dispersoid in cast material homogenizing process.Zr can form the dispersoid of several types.With the highest number density form and therefore normally the dispersoid type of preferred type have Al
3Zr forms and is called Ll
2The atomic arrangement of structure.In the alloy of Al-Mg-Si system, always may not form Ll
2, Al
3Zr, but will form other type dispersoid.Described other type dispersoid can contain Si except that Zr and Al.The Zr dispersoid is main relevant with number density to the influence of extruding Al alloy microscopic structure, and relevant with the dispersoid type on less degree.When the number density of dispersoid is high, extruded material will have fibrous microstructure, and recrystallize will take place the low material of dispersoid number density.The existence of Zr-base dispersoid is similar with the dispersoid of above-mentioned Mn-and Cr-base to the effect of recrystallize material texture, so also causes the high ductility of age hardening material.
Vanadium (V) has the effect that document confirms aspect the ductility that improves the Al-Mg-Si alloy.V can form dispersoid in the Al-Mg-Si alloy, but for as many as 0.1 weight % and addition that may be higher, finds not form a large amount of dispersoids.
Titanium (Ti) adds the grain-size of one side refinement alloy in castingprocesses in the Al alloy usually to boron (B) or carbon (C).In melt, do not add Ti and B or Ti and C separately, but add with previously prepared Al-Ti-B or Al-Ti-C alloy form.Previously prepared Al-Ti-B or Al-Ti-C alloy are commonly called " grain-refining agent ".The Al-Ti-B grain-refining agent contains two class particles usually, and a class is made up of Ti and B substantially and hereinafter these particles is expressed as (Ti, B) particle, and another kind ofly be made up of Ti and Al substantially and hereinafter these particles be expressed as (Al, Ti) particle.The Al-Ti-B grain-refining agent is characterized by the weight ratio of Ti and B content usually, and the Ti/B ratio is generally 2-10.When adding the Al-Ti-B grain-refining agent in melt, (Ti is B) with (Al, Ti) particle is dispersed in the melt, and they serve as the nucleation site of aluminium grain in process of setting when casting.The Al-Ti-C grain-refining agent works in substantially the same mode, and different is that they contain (Ti, C) particle rather than (Ti, B) particle.(International AlloyDesignations and Chemical Composition Limits for WroughtAluminum and Wrought Aluminum Alloy in most of alloy specifications of Al-Mg-Si alloy, The Aluminum Association, Washington DC, USA, in April, 2004), be limited to 0.1-0.2 weight % on the regulation Ti.Yet, realize in the Al-Mg-Si alloy that as everyone knows the required actual Ti content of grain refining is much lower, is typically 0.005-0.03 weight %.
The present inventor finds that Ti also has effect for the ductility of Al-Mg-Si alloy.This needs Ti content to surpass and is used for the Ti content of grain-refining agent, and need Ti surpass from grain-refining agent (Ti, B) and/or (Ti, C) particulate Ti content.Required Ti amount is preferably 0.05-0.20 weight % for 0.03-0.25 weight %.As for V, the Ti addition of the about 0.25 weight % of as many as also may not produce the dispersoid of any significant quantity.Therefore, V is identical probably with the mechanism that Ti improves ductility.
Improve with suitable by the crush properties that adds the Ti acquisition to the Al-Mg-Si alloy by improvement from V acquisition to alloy that add Mn, Cr or.This is confirmed by the following examples:
The Al-Mg-Si alloy that following table 8 provides is tested, and except that element M n, Cr, V, Cu were different with the Ti amount, the Mg of described alloy and Si content were basic identical.
Table 8: embodiment 5 and 6 alloy composition
| Alloy | Mg | Si | Fe | Mn | Cu | V | Cr | Ti |
| B0 | 0.41 | 0.60 | 0.18 | 0.03 | - | - | - | 0.01 |
| B1 | 0.39 | 0.57 | 0.20 | 0.15 | - | 0.08 | - | 0.01 |
| B2 | 0.41 | 0.61 | 0.20 | 0.16 | - | - | 0.06 | 0.01 |
| B3 | 0.40 | 0.60 | 0.20 | 0.16 | - | 0.10 | 0.06 | 0.01 |
| B4 | 0.40 | 0.60 | 0.21 | 0.16 | 0.10 | 0.10 | 0.06 | 0.01 |
| B5 | 0.41 | 0.62 | 0.20 | 0.10 | - | - | 0.06 | 0.02 |
| B6 | 0.42 | 0.64 | 0.22 | 0.16 | - | - | 0.03 | 0.02 |
| B7 | 0.40 | 0.58 | 0.19 | 0.15 | - | - | - | 0.09 |
| B8 | 0.41 | 0.61 | 0.22 | 0.16 | - | - | 0.03 | 0.12 |
| B9 | 0.40 | 0.62 | 0.22 | 0.16 | - | 0.08 | 0.03 | 0.12 |
Carry out the test identical, in forced ventilation, cool off extrusion with embodiment 3.Sample to the age hardening section bar carries out axial pressure break test, provides grade according to table 2.The grade that in Fig. 9, has shown each alloy.
By relatively B0 and alloy variant B2, B5 and B6, Mn and Cr and behavior has positive effect for pressure break without any V or Ti as can be seen.By comparing B2 and B5, can see with B5 and comparing that the Mn that increases has positive effect for the behavior in the pressure break test in B2.Therefore have higher Cr content and have that Cr also is like this in the situation of alloy B 2 of higher pressure break test grade comparing with alloy B 6.Mn among discovery alloy B 2, B3 and the B4 and Cr level are too high so that can not obtain acceptable grain-size, referring to the embodiment among Figure 10 yet in this case.When by the grain-size in any section bar that obtains of alloy B 2, B3 or B4 with for example only have 0.15%Mn and do not have grain-size in the alloy B 1 of Cr relatively the time, find that the grain-size in the alloy B 3 for example is excessive, and may in shaping operation subsequently, cause significant orange peel to produce.Therefore the improvement of the pressure break behavior that can obtain by independent interpolation Mn and Cr is subject to the grain-size requirement that is applied.
By comparing alloy B 1 and B7, find that interpolation V and Ti have approximately uniform positive effect for the behavior in the current pressure break test.By relatively alloy B 2 and B3, V content difference only wherein can be seen the positive effect of V.When comparing alloy B 6 and B8, like this equally for Ti.Therefore V and Ti also produce positive effect except that Mn and Cr positive effect.Because for the amount of adding, V and Ti do not form dispersoid particulate element, therefore estimate to add the problem that these elements can not produce grain-size here.Add several elements when combination in alloy B 9 and for example obtain best behavior when Mn, V, Cr and titanium.
The maximum of addible Ti and V is subjected to can remaining on the amount restriction in the sosoloid in the alloy treatment process.Another factor that must consider is the raising of the deformation resistance that causes of these elements.High-caliber these elements will reduce the extrudability of alloy, and the improvement of pressure break behavior must be considered the reduction of extrudability.At last, owing to compare the higher price of V and Ti with aluminium, therefore represented the cost that increases to alloy interpolation V and Ti.For the present price of V, Ti and Al, add 0.10%V and cause aluminium alloy per ton to increase about 110
And for identical Ti addition, aluminium alloy per ton only increases by 10
Therefore, consider, compare preferred interpolation Ti with V from the cost viewpoint.
Alloy element is for the robustness of ductility effect
Extruding compression ratio and extruding velocity of discharge can noticeable changes between different extruding geometrical shapies.These microstructures that change extruded section have influence, this so that can have influence to the ductility in the pressure break test.In addition, known higher intensity causes relatively poor folding behavior in the axial pressure break test usually.Therefore it is still effective for the change of the variation of the condition of carrying out and intensity with the result of checking embodiment 5 to carry out several groups of tests.
All alloys in the table 8 are squeezed into Fig. 1 b) shown in geometrical shape P3.The extruding compression ratio is 48, and this is the twice of extrusion ratio among the embodiment 5.Adopt two kinds of extrusion speed: 15m/min and 30m/min for the P3 geometrical shape.Because less size and wall thickness, the air cooling of section bar with geometrical shape P3 is faster than the summary of geometrical shape P1 section bar.For the extrusion with geometrical shape P3, be about 1.3 minutes the cooling time in 500-250 ℃ of temperature range.
With extruding and the age hardening of refrigerative section bar to highest hardness and cut into the sample that length is 70mm.Sample is carried out axial pressure break, and specimen length reduces to 32mm thus.Provide grade according to table 2, and shown the grade of each alloy under different condition in Figure 11 and 12.Figure 12 also comprises the yield strength of sample.
Undesirable low value of variant B5 and B6, these results have confirmed the result of embodiment 5 in Figure 11.Once more, the alloy B 1 with 0.10%V has approximately uniform grade with the alloy B 7 with 0.10%Ti after the pressure break test, and this shows that V and Ti have roughly the same effect for ductility.In Figure 12, the result is more as expecting, because alloy variant B5 and B6 have than alloy B 0 better pressure break behavior.
On average, higher than among Figure 11 of the grade after the pressure break test among Figure 12.This is relevant with the grain structure of material to a certain extent.High extrusion speed helps avoiding the texture of coarse crystal of these type alloy, therefore also helps to produce the performance of improving in the pressure break test.When extrusion speed changed, the crush properties that contains the alloy of Ti and/or V changed less on average.
The alloy that provides in the following table 9 is carried out other test.Alloy G0 is identical with alloy B 0 and B5-G9 basically with G5-G9, and just Mg is different with Si content.The Mg of table 9 alloy and Si content this means that a little more than the Mg and the Si content of table 8 interalloy the alloy of table 9 should have the intensity slightly higher than the respective alloy of table 8.Estimate that the bigger alloy of intensity has lower slightly ductility, therefore axially also have lower slightly performance in the pressure break test.
The composition of table 9: embodiment 7 alloys
| Alloy | Mg | Si | Fe | Mn | Cu | V | Cr | Ti |
| G0 | 0.45 | 0.69 | 0.20 | 0.04 | - | - | - | 0.02 |
| G5 | 0.43 | 0.66 | 0.20 | 0.10 | - | - | 0.06 | 0.01 |
| G6 | 0.45 | 0.70 | 0.20 | 0.16 | - | - | 0.03 | 0.01 |
| G7 | 0.45 | 0.67 | 0.20 | 0.16 | - | - | - | 0.13 |
| G8 | 0.45 | 0.68 | 0.21 | 0.16 | - | - | 0.03 | 0.13 |
| G9 | 0.45 | 0.68 | 0.21 | 0.16 | - | 0.08 | 0.03 | 0.13 |
| G10 | 0.45 | 0.68 | 0.21 | 0.16 | 0.05 | 0.10 | 0.03 | 0.13 |
These alloys of extruding under 4 kinds of different conditions:
Geometrical shape P1, extruding velocity of discharge 15m/min, it is cold to carry out shrend after extruding
Geometrical shape P1, extruding velocity of discharge 15m/min, in the laggard line space air cooling of extruding but
Geometrical shape P3, extruding velocity of discharge 15m/min, in the laggard line space air cooling of extruding but
Geometrical shape P3, extruding velocity of discharge 30m/min, in the laggard line space air cooling of extruding but
To push also refrigerative section bar age hardening and arrive highest hardness, and cut into the sample that length is 100mm for geometrical shape P1 then, be the sample of 70mm for geometrical shape P3 Cutting Length.Sample is carried out axial pressure break, thereby for geometrical shape P1 specimen length is reduced to 40mm, P3 reduces to 32mm with specimen length for geometrical shape.Provide grade according to table 2, in Figure 13-16, shown the grade of each alloy under different condition.Figure 13 and Figure 16 also comprise the yield strength of sample.
The alloy G7 and the G6 among Figure 16 in Figure 14, these results have confirmed the result among embodiment 5 and the embodiment 6, add wherein that Mn, Cr, V and Ti provide ductility and the improvement of performance in axial pressure break test.
Summer is than test
Summer is material absorbs the energy ability in failure procedure test than V streak test.Discovery has highly dependency than the amount of energy in the test and during axially pressure break is tested between the behavior in the summer in similar slightly group of alloys.This is confirmed in Figure 17, the figure illustrates grade in the pressure break test of Figure 16 and same material summer than the dependency that absorbs in the test between the energy.Except that comparing the alloy G0 that showed low summer specific energy, be almost linear relationship between the summer specific energy of discovery alloy and the pressure break test grade with pressure break test grade.
In addition, general trend is that the summer specific energy reduces with the alloy strength increase.Consider alloy G0 and G5-G9 in table 8 interalloy B0 and B5-B9 and the table 9.The alloy of table 9 has higher Mg and Si content, therefore reaches the intensity higher than the respective alloy in the table 8 after age hardening.To be squeezed into geometrical shape P3 with velocity of discharge 30m/min and before timeliness air cooled all alloys carry out the summer than the test.The alloy in the table 9 and the difference of yield strength between the respective alloy in the table 8 and summer specific energy in Figure 18, have been shown.Discovery is in this combination gold, and the summer specific energy reduces along with the intensity increase is almost linear.
Consider these dependencys, can think one group of similar slightly alloy is compared that the summer has provided the good indication of they relative behaviors of expection in axially pressure break is tested than test.Provide this comparison among the embodiment 8 below.
The alloy that provides in the his-and-hers watches 10 is tested, and these alloys have essentially identical Mg and Si content, just has different element M n, Cr, V, Cu and Ti content.Alloy X1 is a base alloy, means that other alloy is made up of alloy X1 and additional alloy element.Mg and Si content is a little more than the Mg and the Si content of table 9 interalloy, this means table 10 interalloy in the intensity after the age hardening usually a little more than the intensity of table 9 interalloy after age hardening.
The composition of table 10: embodiment 8 alloys
| Alloy | Mg | Si | Fe | Mn | Cu | V | | Ti |
| X1 | ||||||||
| 0，46 | 0，70 | 0，25 | - | - | - | - | 0，01 | |
| |
0，46 | 0，70 | 0，25 | 0，15 | - | - | - | 0，01 |
| |
0，46 | 0，70 | 0，25 | 0，15 | - | - | 0，06 | 0，01 |
| |
0，46 | 0，70 | 0，25 | 0，15 | - | 0，10 | - | 0，01 |
| |
0，46 | 0，70 | 0，25 | 0，15 | - | - | - | 0，10 |
| |
0，46 | 0，70 | 0，25 | 0，15 | 0，15 | - | - | 0，01 |
| |
0，46 | 0，70 | 0，25 | 0，15 | 0，15 | 0，10 | - | 0，01 |
The flat rod of extruded alloy.Use two kinds of different extruding velocity of discharge, 10m/min and 40m/min.Sample is carried out solution heat treatment, and the cold or air cooling of shrend before age hardening.The material of age hardening is carried out the uniaxial extension test and the summer tests than V indentation.Figure 19 and 20 has shown the summer specific energy that carries out the air cooled section bar of shrend cold-peace before age hardening respectively and the relation of yield strength.Two kinds of extrusion speeds do not cause remarkable difference in Figure 19 and Figure 20.According to table 10, this data form has shown to add which kind of alloy element in base alloy.
For carry out the cold section bar of shrend before age hardening, Figure 19 has shown between the alloy composition of test add Mn+Cr and have the highest favourable influence for the summer specific energy, and interpolation Mn+V and Mn+Ti to have the second high favourable influence for the summer specific energy.
In Figure 20, find identical grade for air cooled section bar before age hardening.Add Mn+Cr and have the highest favourable influence, add Mn+V and have the second high favourable influence, have the 3rd high favourable influence and add Mn+Ti for the summer specific energy.Yet the alloy yield strength that Mn+Cr adds is minimum for having, and the alloy yield strength second that Mn+V adds is low for having, and comprises that for one group of other alloy to have the alloy yield strength the 3rd that Mn+Ti adds low.These differences of intensity can part owing to the difference (referring to Figure 18) of summer specific energy.If three kinds of alloys of all of above-mentioned discussion have identical yield strength, the grade of possibility summer specific energy will remain unchanged so, but the summer specific energy difference between them will be littler.
From embodiment and the discussion that provides herein, the interpolation that can be clear that careful selection alloy element for example Mn, Cr, Zr, V and Ti can significantly improve the ductility and the crush properties of Al-Mg-Si alloy.For the best of breed of performance and workability, it is useful especially that the alloy element (Mn, Cr, Zr) that forms dispersoid is combined with main alloy element (V, Ti) in sosoloid.These principles all are effective for the entire area of Mg in the Al-Mg-Si alloy and Si content.Yet, for working ability with such as the best of breed of the performance of intensity and thermostability, as the initial selection Si that discusses
Eff/ Mg ratio is favourable near 1.4 alloy.Figure 21 shows Mg-Si figure, and wherein drawing equals 1.4 Si/Mg ratio, has also shown the alloy composition for the embodiment of the present invention special concern defined in claim.
Claims (9)
1. have the Al-Mg-Si alloy of good ductility and improvement crush properties, this alloy is specially adapted to the structure unit in the vehicle collision exposed region, it is characterized in that this alloy contains in weight %:
Mg?0.25-1.2
Si?0.3-1.4
Ti 0.1-0.4, wherein Ti is present in the sosoloid, and wherein this alloy also contains one or more following alloy compositions:
Mn maximum 0.6
Cr maximum 0.3
Zr maximum 0.25 and
Idol is deposited impurity, comprises Fe and Zn, and at the most 0.5, surplus is Al.
2. according to the alloy of claim 1, it is characterized in that this alloy also contains one or more following alloy compositions, in weight %:
Cu maximum 0.4 preferred 0.3
V maximum 0.25.
3. according to the alloy of claim 1 and 2, it is characterized in that this alloy contains 0.1-0.3Ti in weight %, and preferred 0.1-0.2Ti.
4. according to the alloy of claim 1-3, it is characterized in that alloy composition is limited in the following coordinate point of Mg-Si figure:
a1-a2-a3-a4-a1
Wherein in weight %, a1=0.25Mg, 0.55Si, a2=0.50Mg, 1.0Si, a3=0.75Mg, 0.75Si and a4=0.45Mg, 0.40Si.
5. according to the alloy of claim 4, it is characterized in that this alloy is limited in the coordinate point b1-b2-b3-b4-b1, wherein in weight %, b1=0.30Mg, 0.60Si, b2=0.50Mg, 0.90Si, b3=0.65Mg, 0.75Si and b4=0.45Mg, 0.50Si.
6. according to the alloy of claim 5, it is characterized in that this alloy more preferably is limited between the coordinate point c1-c2-c3-c4-c1, wherein in weight %, c1=0.33Mg, 0.60Si, c2=0.47Mg, 0.80Si, c3=0.59Mg, 0.70Si and c4=0.45Mg, 0.52Si.
7. according to the alloy of claim 1-6, it is characterized in that this alloy contains in weight %:
Mn?0.05-0.30
Cr maximum 0.05
Zr maximum 0.15.
8. according to the alloy of claim 1-7, it is characterized in that this alloy casting is become briquet, carry out homogenizing then.
9. according to the alloy of claim 1-8, it is characterized in that this alloy is heated to preferred temperature once more, then extruding.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| NO20060794 | 2006-02-17 | ||
| NO20060794 | 2006-02-17 |
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| US (1) | US20090116999A1 (en) |
| EP (1) | EP1987170A1 (en) |
| JP (1) | JP2009526913A (en) |
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2007
- 2007-02-16 WO PCT/NO2007/000057 patent/WO2007094686A1/en active Application Filing
- 2007-02-16 EP EP07715944A patent/EP1987170A1/en not_active Withdrawn
- 2007-02-16 JP JP2008555185A patent/JP2009526913A/en not_active Withdrawn
- 2007-02-16 CN CNA2007800058797A patent/CN101384741A/en active Pending
- 2007-02-16 US US12/224,035 patent/US20090116999A1/en not_active Abandoned
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2007094686A1 (en) | 2007-08-23 |
| JP2009526913A (en) | 2009-07-23 |
| EP1987170A1 (en) | 2008-11-05 |
| US20090116999A1 (en) | 2009-05-07 |
| WO2007094686A8 (en) | 2008-09-25 |
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