WO2016207274A1 - Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung - Google Patents
Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung Download PDFInfo
- Publication number
- WO2016207274A1 WO2016207274A1 PCT/EP2016/064530 EP2016064530W WO2016207274A1 WO 2016207274 A1 WO2016207274 A1 WO 2016207274A1 EP 2016064530 W EP2016064530 W EP 2016064530W WO 2016207274 A1 WO2016207274 A1 WO 2016207274A1
- Authority
- WO
- WIPO (PCT)
- Prior art keywords
- aluminum alloy
- strip
- rolling
- alloy strip
- weight
- Prior art date
Links
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 24
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 146
- 238000000137 annealing Methods 0.000 claims abstract description 60
- 238000000034 method Methods 0.000 claims abstract description 28
- 238000005097 cold rolling Methods 0.000 claims abstract description 24
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 14
- 238000005098 hot rolling Methods 0.000 claims abstract description 11
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 9
- 239000012535 impurity Substances 0.000 claims abstract description 7
- 229910052751 metal Inorganic materials 0.000 claims abstract description 7
- 239000002184 metal Substances 0.000 claims abstract description 7
- 238000005266 casting Methods 0.000 claims abstract description 4
- 230000007797 corrosion Effects 0.000 claims description 42
- 238000005260 corrosion Methods 0.000 claims description 42
- 238000005096 rolling process Methods 0.000 claims description 30
- 206010070834 Sensitisation Diseases 0.000 claims description 7
- 230000008313 sensitization Effects 0.000 claims description 7
- 239000000470 constituent Substances 0.000 claims description 4
- 238000005275 alloying Methods 0.000 claims description 3
- 239000000725 suspension Substances 0.000 claims 1
- 230000009467 reduction Effects 0.000 abstract description 4
- 229910052802 copper Inorganic materials 0.000 abstract description 2
- 229910052719 titanium Inorganic materials 0.000 abstract description 2
- 229910052725 zinc Inorganic materials 0.000 abstract description 2
- 229910052742 iron Inorganic materials 0.000 abstract 1
- 238000003825 pressing Methods 0.000 abstract 1
- 239000011572 manganese Substances 0.000 description 17
- 239000011651 chromium Substances 0.000 description 14
- 230000000052 comparative effect Effects 0.000 description 12
- 239000011777 magnesium Substances 0.000 description 12
- 230000006399 behavior Effects 0.000 description 9
- 229910052748 manganese Inorganic materials 0.000 description 7
- 239000000463 material Substances 0.000 description 6
- 239000000203 mixture Substances 0.000 description 6
- 238000000465 moulding Methods 0.000 description 6
- 239000010936 titanium Substances 0.000 description 6
- 230000000694 effects Effects 0.000 description 5
- 238000002474 experimental method Methods 0.000 description 5
- 239000011701 zinc Substances 0.000 description 5
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 4
- 239000010949 copper Substances 0.000 description 4
- 239000002245 particle Substances 0.000 description 3
- 238000011084 recovery Methods 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 230000002411 adverse Effects 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 229910052749 magnesium Inorganic materials 0.000 description 2
- 238000005482 strain hardening Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 description 1
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 1
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 238000006243 chemical reaction Methods 0.000 description 1
- 239000007795 chemical reaction product Substances 0.000 description 1
- 239000003795 chemical substances by application Substances 0.000 description 1
- 238000010276 construction Methods 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 230000008602 contraction Effects 0.000 description 1
- 238000003618 dip coating Methods 0.000 description 1
- 238000009826 distribution Methods 0.000 description 1
- 239000004615 ingredient Substances 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 229910052706 scandium Inorganic materials 0.000 description 1
- SIXSYDAISGFNSX-UHFFFAOYSA-N scandium atom Chemical compound [Sc] SIXSYDAISGFNSX-UHFFFAOYSA-N 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 208000016261 weight loss Diseases 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
Classifications
-
- 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
-
- 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
-
- 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
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
Definitions
- the invention relates to a method for producing an aluminum strip or sheet from an aluminum alloy and an aluminum alloy strip or sheet and its use.
- Aluminum alloy sheets are playing an increasing role as compared to
- Aluminum sheets made of a hardenable Al-Mg-Si alloy of class AA6XXX Aluminum alloy sheets of this class are used in the solution-treated state T4 and then subjected to a heat aging to achieve a higher ultimate strength in the state T6.
- AlMg alloys of the type AA 5xxx with Mg contents of more than 3% by weight, in particular more than 4% by weight, are increasingly prone to intercrystalline corrosion, for example when exposed to elevated temperatures.
- ⁇ -AlsMg3 phases precipitate along the grain boundaries, which are referred to as ⁇ -particles and can be selectively dissolved in the presence of a corrosive medium.
- Standard test according to ASTM G67 in which the samples are exposed to nitric acid and the mass loss of the aluminum sheet is measured.
- ASTM G67 Standard test according to ASTM G67, in which the samples are exposed to nitric acid and the mass loss of the aluminum sheet is measured.
- ASTM G67 a corresponding heat load of the components in the application is simulated by a prior sensitization annealing at temperatures of 130 ° C. for 17 hours.
- the mass loss for materials which are not resistant to intergranular corrosion is more than 15 mg / cm 2 .
- the production of an intercrystalline corrosion resistant
- WO 2014/029853 Al Although the aluminum alloy sheets disclosed herein have a good tensile strength R m and excellent values for the uniform elongation A g with good resistance to intergranular corrosion. However, the values for the yield strength R p0 , 2, which is a measure of the resistance of the sheet to plastic deformation, are too low to significantly reduce the yield
- Aluminum alloy sheets are from the cited German Offenlegungsschrift not known.
- information on specific mechanical properties of a work hardened and Weggeglühten aluminum alloy strip in said German patent application are not disclosed.
- the object of the present invention is to propose an aluminum alloy strip or sheet made of a hardenable aluminum alloy which, in addition to a high weight saving potential in the motor vehicle, can be produced inexpensively.
- the aforementioned object solves a method for producing an aluminum strip or sheet from a
- Aluminum alloy strip at 300 ° C to 500 ° C, such that the cold-rolled aluminum alloy strip has a recrystallized structure after the intermediate annealing,
- Metal temperature is 190 - 250 ° C for at least 0.5 h.
- sheets can then be tinned from the aluminum alloy strip.
- the magnesium content of the aluminum alloy to be used according to the invention is from 3.6% by weight to 6% by weight, preferably from 4.2% by weight to 6% by weight, particularly preferably from 4.2% by weight to 5 , 2 wt .-% contributes to the fact that the aluminum alloy with good forming properties at the same time high
- Strength values in particular yield strength R p0 , 2 and tensile strength R m achieved. Unwanted hardening and precipitation effects of Si are reduced by limiting the Si content to a maximum of 0.4% by weight.
- the Fe content should be limited to a maximum of 0.5% by weight. This also applies to the copper content, which should be limited to a maximum of 0.15 wt .-%.
- Manganese leads to an increase in strength and also to an improvement in the resistance to intergranular corrosion. However, the manganese content must be limited because otherwise the forming properties of the annealed
- Forming properties such as the uniform strain A g or the
- Fractional contraction Z decrease, so that the forming properties are deteriorated. Furthermore, Cr also leads to small grain sizes after the intermediate annealing.
- the chromium content should be limited to values of less than 0.05% by weight, preferably less than 0.01% by weight.
- Zr which, since it usually has to be added, is not listed here in detail.
- Zinc could have a negative effect on the corrosion resistance of the aluminum alloy strip and should therefore be limited to a maximum of 0.2% by weight.
- Titanium is commonly added in continuous casting of the aluminum alloy as a grain refining agent, for example in the form of Ti-boride wire or rods.
- too high Ti contents in turn have a negative effect on the forming properties, so that a limitation of the Ti content to a maximum of 0.20 wt .-% is desired.
- a roll bar for hot rolling By casting and homogenizing the rolling ingot at 480 ° C to 550 ° C for at least 0.5 hours, a roll bar for hot rolling can be provided which has a very homogeneous distribution of the alloy components.
- a homogeneous recrystallized hot strip is provided by hot rolling in a temperature range of 280 ° C to 500 ° C.
- the degree of rolling during cold rolling is
- Aluminum alloy strip according to the invention only 10% to 45%, since the Abwalzgrad before the last intermediate annealing the emergence of the grain structure
- the intermediate annealing allows the provision of a recrystallized microstructure for the last one
- Cold rolling step which is carried out with a degree of rolling of 30% to 60% of final thickness.
- the final rolling degree allows, in contrast to
- Aluminum alloy strip by work hardening to the desired application, for example, to a yield strength of more than 190 MPa after the
- Aluminum alloy tape can be provided, on the one hand good, for example, can be converted to a vehicle component and on the other hand provides high yield strengths in the non-formed areas.
- the produced aluminum alloy strip is at the same time also resistant to intercrystalline
- the degree of rolling is limited to 20% to 30%, larger grain diameters are provided in the aluminum alloy strip after the last intermediate annealing and thus the resistance to
- the yield strength R p0 , 2 can be set to values above 200 MPa, without the forming properties, for example, the uniform elongation A g or .
- Providing aluminum alloy tapes and sheets for conversion to vehicle components such as body-in-white (BIW) components.
- vehicle components such as body-in-white (BIW) components.
- the aluminum alloy strip when the aluminum alloy strip is cold rolled to a thickness of 0.5 mm to 5.0 mm, preferably to 1.0 mm to 3.0 mm final thickness, moldings may be produced from a non-hardenable aluminum alloy for vehicle components, which cost
- the temperature during the annealing of the aluminum alloy strip is 220 ° C to 240 ° C.
- Aluminum alloy strip produced components in case of any thermal stress during operation.
- the above object is achieved by a cold-rolled and re-annealed aluminum alloy strip or sheet, which is preferably made by the method of the invention, consisting of an aluminum alloy with the following
- Aluminum Alloy Composition Yield Strings Rp0.2 of greater than 190 MPa to 300 MPa with a uniform elongation of 14% to 18% and a
- the Mg content of the aluminum alloy strip or sheet may be 4.2% by weight to 6% by weight, preferably 4.2% by weight to 5.2% by weight
- Aluminum alloy ribbon or sheet limited to 0.1 wt .-% to 0.3 wt .-%, so can despite the positive influence of manganese on the strength and
- Corrosion resistance of aluminum alloy strip or sheet at the same time good forming properties, ie high values for uniform elongation A g and the
- Grain diameter of more than 20 ⁇ be set reliably, which positively affect the corrosion resistance of the aluminum alloy strip or sheet.
- the chromium content negatively affects the properties of the aluminum alloy even at very low concentrations with respect to the forming behavior and limits the grain size after the last intermediate annealing so that, according to another embodiment of the aluminum alloy strip or sheet, the chromium content is reduced to less is limited as 0.01 wt .-%. This also applies analogously to zirconium and scandium which, if at all, are only present in traces in the aluminum alloy.
- the aluminum alloy strip or sheet has one or more of the following limitations on the proportions of
- Aluminum alloy strip or sheet the aluminum alloy strip has one or more of the following characteristics:
- the aluminum alloy strip can be manufactured by adjusting the specific properties of yield strength, uniform elongation, fracture constriction and behavior in the corrosion test in addition to the different fields of application. For example, a higher yield strength of more than 200 MPa can reduce the final thicknesses of the aluminum alloy strip and thus a allow further reduction of the weight of the molding produced therefrom, for example a vehicle component.
- the increase in the uniform expansion to at least 15% or the increase in the Brucheinschnürung Z to at least 55% means that the aluminum alloy strip or sheet according to the invention can be used in complex forming processes and, for example, complex shaped moldings can be produced with a few forming steps.
- Corrosion test according to ASTM G67 in turn leads to increased safety against failure due to intercrystalline corrosion of a molded part produced from the aluminum alloy strip.
- Aluminum alloy strip or sheet according to the present embodiment a significantly increased field of application due to the greatly improved
- the above object is also achieved by the use of an aluminum alloy strip or sheet according to the invention for the production of structural parts or vehicle components, in particular BIW components of a motor vehicle, since the aluminum alloy strips according to the invention allow the production of molded parts for the corresponding use, which undergo very high degrees of deformation At the same time, however, they can provide high yield strengths for reducing the material thickness of the aluminum alloy strip or sheet and nevertheless have a very good corrosion behavior in the corrosion test according to ASTM G67.
- the invention will be explained in more detail with reference to embodiments in conjunction with the drawings.
- the drawing shows in Fig. 1 in a schematic representation of the method steps of an embodiment of the method for producing an aluminum alloy strip and
- FIG. 1 initially shows the method steps of a schematic representation
- step 1 a
- Rolling bar consisting of an aluminum alloy with the following
- the ingot is homogenized for a period of at least 0.5 h according to step 2.
- This is followed by the Hot rolling the rolling ingot in step 3 at a temperature of 280 ° C to 500 ° C to a hot strip.
- the limitation of Abwalzgrads to 10% to 45% causes in the subsequent intermediate annealing according to step 5 by recrystallization a mean grain size of more than 20 ⁇ can be achieved.
- the implementation of the last intermediate annealing of the cold-rolled aluminum alloy strip at 300 ° C to 500 ° C provides for the final cold rolling step 6, a recrystallized structure with grain sizes of more than 20 ⁇ available. Steps 4 and 5 can possibly
- step 6 the cold rolling according to step 6 at a degree of rolling of 30% to 60% of the final thickness, cold work hardening is introduced into the recrystallized structure, which leads to an increase in the yield strength R p0 , 2 .
- step 7 the cold-rolled structure is subjected to a recovery, so that in particular the
- the manufactured uniform elongation A g of more than 14% and values for the fracture waist Z of more than 50% the manufactured
- BIW components are often converted into shaped parts, for example to vehicle components of the "body-in-white" of a motor vehicle, so-called BIW components.
- BIW components often have complex geometries and therefore require a high degree of reshapability of the belts or belts Sheets from which they are made
- BIW components made of an aluminum alloy also require correspondingly low sheet thicknesses, which is high
- Aluminum alloy strips according to the invention and the sheets produced therefrom fulfill this requirement as well as the necessary corrosion resistance, as experiments show.
- Be vehicle components, in particular BIW components therefore from an inventive
- FIG. 2a) and 2b) show schematically areas of application of the invention
- Corrosion behavior of the aluminum alloy strips according to the present invention opens up further applications for the
- Table 1 shows a total of seven different ones
- Experiments 1, 2 and 9 included aluminum alloys whose Mg, Mn or Cr content are outside the range according to the invention.
- the Mg content is too small and the contents of Mn and Cr are too large. Too high values for Cr and slightly increased values for Mn also include Comparative Example No. 2.
- Comparative Example No. 9 in turn has clearly too large values for Mn and Cr. The hot strips made of different aluminum alloys were then cold rolled before the last one according to the specifications in Table 2
- Annealing temperature was 240 ° C in all experiments. The annealing was carried out in the coil, wherein the metal temperature of the annealing temperature was maintained for a period of at least 0.5 h.
- Table 2 also indicates the final thicknesses a 0 , which are approximately between 0.7 mm and 1.7 mm. In Table 2, the Abwalzgrade which are outside the range of the invention, underlined. Comparative Examples Nos. 1 and 6 have excessive degrees of finish before intermediate annealing, whereas Comparative Example No. 3 has too low final rolling degree after intermediate annealing.
- the mean grain size ie the average grain diameter, was measured. For this purpose, samples were taken from the tapes and anodized longitudinal blanks according to the Barker method. Under the microscope, the samples were measured according to ASTM E1382 and the mean grain size determined by the mean grain diameter.
- Table 3 also shows the mass loss values in a corrosion test according to ASTM G67 (NAMLT), in which the samples were previously subjected to a simulated thermal stress for 17 hours at 130 ° C.
- NAMLT ASTM G67
- Comparative Example No. 1 which has a markedly increased Mn content, for example, the uniform elongation A g decreases to 10.6%. Also, the too low Mg content of Comparative Example No. 1 counteracts large elongation values.
- Comparative Example No. 2 having an increased Cr content at a slightly excessive Mn content shows fracture necking values Z that are less than 50%, indicating a deteriorated forming performance.
- Fracture necking Z represents precisely the property of the material, in the case of large deformations via a cross-sectional reduction material for the forming to provide without tearing. Due to the higher Mn contents or Cr contents, the average particle size of 10 or 15 ⁇ m has no negative influence on the corrosion properties of these samples. Comparing Comparative Example No. 3 with the invention
- Exemplary embodiment No. 4 makes it clear that the yield point R p0 , 2 can be set via the adjustment of the degree of rolling during final rolling after the intermediate annealing .
- Embodiments Nos. 4, 5 and 8 show that about
- the yield strength R p o, 2 can be increased to values up to 211 MPa without causing significant losses in the area of the characteristic values for the transformation, such as the uniform elongation A g or Z.
- Aluminum alloy as Examples 3, 4, 5 and 8 can be very clearly recognized the influence of the adjustment of the average grain diameter by limiting the degree of rolling during cold rolling before the last intermediate annealing.
- the intermediate annealing produces a relatively fine grain having an average diameter or an average grain size of 13 ⁇ m, which produces the
- Comparative Example No. 6 is classified as not resistant to intergranular corrosion.
- the embodiments according to the invention show that the yield strength R p o, 2 are increased to values of up to 270 MPa by using degrees of rolling in final cold rolling of 40% to 60%.
- the higher Mg content of up to 5.2 wt .-% in the embodiment no. 12 contributes to the significant increase in the yield strength R p o, 2 at.
- a comparison of the embodiments of the invention No. 9, 10 and 11 shows that the corrosion resistance depends strongly on the choice of Abwalzgrades before the last intermediate annealing and thus from the mean grain diameter or the average grain size.
- the Mg content is increased over Embodiment No. 9, which in principle may lead to inferior corrosion resistance to intergranular corrosion.
- Aluminum alloy strip can be provided which
- Vehicle components is particularly well suited and can be produced inexpensively due to the use of non-hardenable aluminum alloy.
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Metal Rolling (AREA)
Abstract
Description
Claims
Priority Applications (8)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP16732581.0A EP3314031B1 (de) | 2015-06-25 | 2016-06-23 | Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung |
KR1020187002189A KR101911037B1 (ko) | 2015-06-25 | 2016-06-23 | 고강도이며 용이하게 성형 가능한 almg-스트립 및 그 제조 방법 |
JP2017566413A JP6481052B2 (ja) | 2015-06-25 | 2016-06-23 | 高強度かつ容易に成形可能なAlMgストリップおよび同を製造するための方法 |
CN201680037164.9A CN107787376A (zh) | 2015-06-25 | 2016-06-23 | 高强度且成形优良的AlMg带材及其生产方法 |
ES16732581T ES2700140T3 (es) | 2015-06-25 | 2016-06-23 | Banda de AlMg de alta resistencia y adecuadamente conformable así como procedimiento para su fabricación |
RU2018102706A RU2685295C1 (ru) | 2015-06-25 | 2016-06-23 | Высокопрочная, легкодеформируемая алюминиево-магниевая полоса и способ её получения |
CA2990303A CA2990303C (en) | 2015-06-25 | 2016-06-23 | High-strength and easily formable almg-strip, and method for producing the same |
US15/849,387 US11352686B2 (en) | 2015-06-25 | 2017-12-20 | High-strength and easily formable AlMg-strip, and method for producing the same |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
EP15173888 | 2015-06-25 | ||
EP15173888.7 | 2015-06-25 |
Related Child Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
US15/849,387 Continuation US11352686B2 (en) | 2015-06-25 | 2017-12-20 | High-strength and easily formable AlMg-strip, and method for producing the same |
Publications (1)
Publication Number | Publication Date |
---|---|
WO2016207274A1 true WO2016207274A1 (de) | 2016-12-29 |
Family
ID=53498817
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
PCT/EP2016/064530 WO2016207274A1 (de) | 2015-06-25 | 2016-06-23 | Hochfestes und gut umformbares almg-band sowie verfahren zu seiner herstellung |
Country Status (9)
Country | Link |
---|---|
US (1) | US11352686B2 (de) |
EP (1) | EP3314031B1 (de) |
JP (1) | JP6481052B2 (de) |
KR (1) | KR101911037B1 (de) |
CN (1) | CN107787376A (de) |
CA (1) | CA2990303C (de) |
ES (1) | ES2700140T3 (de) |
RU (1) | RU2685295C1 (de) |
WO (1) | WO2016207274A1 (de) |
Cited By (3)
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CN113981282A (zh) * | 2021-10-28 | 2022-01-28 | 中铝西南铝板带有限公司 | 一种液晶背光模组背板用铝合金带材及其制备方法和应用 |
CN115369293A (zh) * | 2022-04-08 | 2022-11-22 | 中铝瑞闽股份有限公司 | 一种高强度阳极氧化用Al-Mg系铝板带及其制备方法 |
WO2023031334A1 (de) * | 2021-09-03 | 2023-03-09 | Speira Gmbh | Umformoptimiertes aluminiumlegierungsband und verfahren zur herstellung |
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HUE060741T2 (hu) * | 2018-06-11 | 2023-04-28 | Novelis Koblenz Gmbh | Al-Mg-Mn ötvözetbõl készült, fokozott korrózióellenállással rendelkezõ lemeztermék elõállításának módszere |
FR3085968B1 (fr) * | 2018-09-13 | 2022-08-12 | Constellium Issoire | PRODUIT EN ALLIAGE AlMgMn A TENUE A LA CORROSION AMELIOREE |
CN109321790B (zh) * | 2018-12-06 | 2020-10-02 | 中铝瑞闽股份有限公司 | 一种土司盒用铝基材及其制备方法 |
EP3690076A1 (de) * | 2019-01-30 | 2020-08-05 | Amag Rolling GmbH | Verfahren zur herstellung eines blechs oder bands aus einer aluminiumlegierung sowie ein dadurch hergestelltes blech, band oder formteil |
EP3741875A1 (de) * | 2019-05-24 | 2020-11-25 | Constellium Rolled Products Singen GmbH & Co.KG | Aluminiumlegierungsblechprodukt mit verbesserter oberflächengüte |
CN110343919A (zh) * | 2019-07-18 | 2019-10-18 | 哈尔滨理工大学 | 一种质量轻硬度大强度高的铝合金及其制备方法 |
WO2021064260A1 (es) * | 2019-10-04 | 2021-04-08 | Acr Ii Aluminium Group Cooperatief U.A. | Procedimiento para proteger un metal durante un proceso de recocido y producto metálico obtenido |
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RU2749101C1 (ru) * | 2020-08-07 | 2021-06-04 | Федеральное государственное бюджетное учреждение науки Самарский федеральный исследовательский центр Российской академии наук (СамНЦ РАН) | СПОСОБ ХОЛОДНОЙ МНОГОПРОХОДНОЙ ПРОКАТКИ ТОНКИХ ЛЕНТ ИЗ АЛЮМИНИЕВЫХ СПЛАВОВ Al-Mg |
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WO2023031334A1 (de) * | 2021-09-03 | 2023-03-09 | Speira Gmbh | Umformoptimiertes aluminiumlegierungsband und verfahren zur herstellung |
CN113981282A (zh) * | 2021-10-28 | 2022-01-28 | 中铝西南铝板带有限公司 | 一种液晶背光模组背板用铝合金带材及其制备方法和应用 |
CN115369293A (zh) * | 2022-04-08 | 2022-11-22 | 中铝瑞闽股份有限公司 | 一种高强度阳极氧化用Al-Mg系铝板带及其制备方法 |
CN115369293B (zh) * | 2022-04-08 | 2023-08-18 | 中铝瑞闽股份有限公司 | 一种高强度阳极氧化用Al-Mg系铝板带及其制备方法 |
Also Published As
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JP2018524468A (ja) | 2018-08-30 |
CA2990303C (en) | 2019-12-17 |
KR101911037B1 (ko) | 2018-10-23 |
US20180112297A1 (en) | 2018-04-26 |
ES2700140T3 (es) | 2019-02-14 |
RU2685295C1 (ru) | 2019-04-17 |
US11352686B2 (en) | 2022-06-07 |
CA2990303A1 (en) | 2016-12-29 |
JP6481052B2 (ja) | 2019-03-13 |
EP3314031A1 (de) | 2018-05-02 |
CN107787376A (zh) | 2018-03-09 |
KR20180016608A (ko) | 2018-02-14 |
EP3314031B1 (de) | 2018-11-07 |
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