EP1945825A1 - Al-cu-mg-legierung, die für raumfahrtanwendungen geeignet ist - Google Patents

Al-cu-mg-legierung, die für raumfahrtanwendungen geeignet ist

Info

Publication number
EP1945825A1
EP1945825A1 EP06818278A EP06818278A EP1945825A1 EP 1945825 A1 EP1945825 A1 EP 1945825A1 EP 06818278 A EP06818278 A EP 06818278A EP 06818278 A EP06818278 A EP 06818278A EP 1945825 A1 EP1945825 A1 EP 1945825A1
Authority
EP
European Patent Office
Prior art keywords
aluminium alloy
product
alloy product
processed
alloy
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP06818278A
Other languages
English (en)
French (fr)
Other versions
EP1945825B1 (de
Inventor
Paola Valentina Absala Morra
Martinez Carlos Ernesto Caicedo
Jörgen VAN DE LANGKRUIS
Johan Boezewinkel
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Novelis Koblenz GmbH
Original Assignee
Aleris Aluminum Koblenz GmbH
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
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Application filed by Aleris Aluminum Koblenz GmbH filed Critical Aleris Aluminum Koblenz GmbH
Priority to EP06818278.1A priority Critical patent/EP1945825B1/de
Publication of EP1945825A1 publication Critical patent/EP1945825A1/de
Application granted granted Critical
Publication of EP1945825B1 publication Critical patent/EP1945825B1/de
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Links

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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium

Definitions

  • the invention relates to an aluminium wrought alloy, in particular an Al-Cu- Mg type alloy (or AA2000 series aluminium alloy as designated by the Aluminium
  • the present invention relates to an aluminium alloy product having high strength, high fracture toughness exhibiting low crack propagation and high resistance to intergranular corrosion.
  • Products made from the aluminium alloy according to the invention are very suitable for aerospace applications but not limited thereto.
  • the alloy can be processed to various product forms such as sheet, thin plate or an extruded product, a forged product, or a welded product.
  • the aluminium alloy product can be uncoated or coated or plated with another aluminium alloy in order to improve desired properties even further.
  • AA2000 series aluminium alloys in aeroplanes is as fuselage or skin plate, for which purpose typically AA2024 in the T351 temper is used or as lower wing plate for which purpose typically AA2024 in the T351 temper and AA2324 in the T39 temper is used.
  • Intergranular corrosion of an aluminium alloy not only affects the integrity of the structure for which it is used, in which may corroded grain boundaries may act as a nucleus for cracks which propagate under the influence of the alternating load during operation of the structure. Therefore, the occurrence of intergranular corrosion sets limits to the use of aluminium alloys of the AA2000 series with high levels of the mentioned alloying elements.
  • the most commonly used aluminium alloys form the AA2000 series for aerospace application are AA2024, AA2024HDT ("High Damage Tolerant") and AA2324.
  • the present invention is directed to a AA2000 series aluminium alloy having the capability of achieving a balance of properties in any relevant product made of the alloy that is better than the balance of properties of the variety of commercially available aluminium alloys of the AA2000 series, nowadays used for such a product or of AA2000 series aluminium alloys disclosed so far.
  • One object of the present invention is to provide an aluminium alloy wrought product, in particular suitable for aerospace application within the AA2000 series alloys having an improved balance of high strength and fracture toughness and high resistance to intergranular corrosion.
  • Another object of the present invention is to provide an aluminium alloy wrought product as referred to above which shows a high resistance to exfoliation corrosion and stress corrosion cracking.
  • a further object of the present invention is to provide an aluminium alloy wrought product as referred to above which is tolerant to the usual variation in process parameters during its manufacturing process.
  • Yet another object of the present invention is to provide an aluminium alloy wrought product as referred to above which is weldable and suitable for use in welded constructions.
  • Yet another object of the present invention is to provide an aluminium wrought product as referred to above in a form which is suitable for use in an aerospace structure.
  • a further object of the present invention is to provide a method of manufacturing an aluminium alloy wrought product as mentioned hereinabove.
  • an aluminium alloy wrought product having high strength and high fracture toughness and high resistance to intergranular corrosion, the aluminium alloy comprising in weight %:
  • Fig. 1 shows a Cr-Ti diagram setting out the Cr-Ti range for the invention together with narrower preferred ranges.
  • Figs. 2a, 2b show micrographs of a cross section of a sample of an alloy according to the invention in T3 temper and of a comparative alloy after corrosion testing.
  • Figs. 3a, 3b show micrographs of a cross section of a sample of an alloy according to the invention in T6 temper and of a comparative alloy after corrosion testing.
  • the present invention provides an aluminium alloy wrought product having high strength and high fracture toughness and high resistance to intergranular corrosion, the aluminium alloy comprising in weight %:
  • composition of the aluminium alloy according to our invention leads to an alloy product having a high resistance to intergranular corrosion while maintaining a higher strength and higher toughness as compared to the conventional AA2024 alloy.
  • the alloy product of the invention also exhibits a high resistance to exfoliation corrosion and stress corrosion cracking.
  • Good results are also obtained in a preferred embodiment of the invention wherein 0.03% ⁇ Ti ⁇ 0.3%, preferably 0.05% ⁇ Ti ⁇ 0.2%. According to this embodiment good properties can also be achieved with a lower concentration of Ti.
  • Another embodiment has the range wherein 0.05% ⁇ Cr ⁇ 0.3%, preferably
  • a further embodiment has the range wherein 0.1% ⁇ Ti + Cr ⁇ 0.4%. It has been found that within the given range Ti and Cr can be substituted by each other while maintaining good resistance against intergranular corrosion and good mechanical properties.
  • the Cu level is selected in the range wherein 4.4% ⁇ Cu ⁇ 5.5%, more preferably 4.7% ⁇ Cu ⁇ 5.3%.
  • the Mg level is selected in the range wherein 0.3% ⁇ Mg ⁇ 1.2%, more preferably 0.4% ⁇ Mg ⁇ 0.75%.
  • Iron can be present in the range of up to 0.20% and preferably is kept to a maximum of 0.15%, more preferably to a maximum of 0.1%.
  • a typical preferred iron level would be in the range of 0.03% to 0.08%.
  • Silicon can be present in a range of up to 0.20% and preferably is kept to a maximum of 0.15%, more preferably to a maximum of 0.1%.
  • a typical preferred silicon level would be as low as possible and would typically be for practical reasons in a range of 0.02% to 0.07%.
  • Zirconium can be present in the alloy product according to the invention in an amount of up to 0.20%.
  • a suitable Zr level is a range of 0.04% to 0.15%.
  • a more preferred upper limit for the Zr level is 0.13%, and even more preferably not more than 0.11%.
  • Manganese can be added alone or in combination with other dispersoid formers.
  • a preferred maximum for the Mn level is 0.80% and a preferred minimum level is 0.15%.
  • a preferred range for the Mn level is in the range of wherein 0.2% ⁇ Mn ⁇ 0.5%.
  • a second drawback is that also in relation to the price of Ag, any scrap of the alloy should be carefully handled and recycled to reclaim the Ag.
  • the alloy is free of Ag.
  • the alloy is substantially free of Ag. With “substantially free” is meant that no purposeful addition of Ag was made to the chemical composition but that due to impurities and/or leaking from contact with manufacturing equipment, trace quantities of Ag may nevertheless find their way into the aluminium alloy product.
  • the alloy has a composition consisting of, in wt.%:
  • Si ⁇ 0.15% preferably ⁇ 0.1%, and the balance being aluminium and other impurities or incidental elements each ⁇ 0.05%, total ⁇ 0.15%, and is substantially free of Ag. More preferred narrower ranges for the various alloying elements are set out in this specification and claims.
  • the aluminium alloy product according to the invention is in the T3x, T6x or T8x temper.
  • the appropriate temper is selected to give the alloy product desired properties. Temper designations are according to the Aluminium Association.
  • the product is preferably provided in the form of a sheet, plate, forging or extrusion for use in an aerospace structure.
  • the aluminium alloy product according to the invention shows an excellent balance of properties for application as plate over a wide variety of thickness, preferably in the form of a plate having a thickness in the range of 0.7 to 80 mm. In the plate thickness range of 0.6 to 1.5 mm the aluminium alloy product is also of particular interest as automotive body sheet.
  • the properties of the aluminium alloy product will be excellent for fuselage sheet and preferably the thickness is up to 25 mm.
  • the properties are excellent for wing plates, e.g. lower wing plate, when tensile strength and fatigue properties are of great importance.
  • the aluminium alloy products can also be used for stringers or to form an integral wing panel and stringer for use in an aircraft wing structure.
  • aluminium alloy product according to the invention can also be used as tooling plate or mould plate, e.g. for moulds for manufacturing formed plastic products for example via die-casting or injection moulding.
  • higher Fe and Si levels up to 0.4% for each of these elements are acceptable.
  • the invention is also embodied in a method for the manufacture of an aluminium alloy product having high strength and high fracture toughness and a high resistance to intergranular corrosion comprising the steps of: a. casting an ingot having a composition according to the invention; b. homogenising and/or pre-heating the ingot after casting; c. hot working the ingot into a worked product by one of more methods selected from the group consisting of rolling, extruding and forging; d. optional reheating the worked product, and e. optional further hot working and/or cold working to a desired work piece form; f. solution heat treating said formed work piece at a temperature and time sufficient to place into solid solutions substantially all soluble constituents in the alloy; g.
  • the method according to the invention yields aluminium alloy product having excellent resistance to intergranular corrosion and having high strength and excellent fatigue properties.
  • the alloy products of the present invention are regularly prepared by melting and alloying an aluminium alloy product and may be direct chill (“D. C") cast into ingots or other suitable casting techniques. Homogenisation treatment is typically carried out in one or more steps, each step having a temperature preferably in the range of 46O 0 C to 535 0 C.
  • the pre-heat temperature involves heating the ingot to the hot working temperature which is typically in a temperature range of 400 0 C to 48O 0 C.
  • Working the alloy product can be done by one or more methods selected from the group consisting of rolling, extruding and forging. For the present alloy product hot rolling is preferred. Solution heat treatment is typically carried out in the same temperature range as used for homogenisation although somewhat shorter soaking times can be selected.
  • artificial ageing preferably comprises an ageing step at a temperature in the range of 135 0 C to 21O 0 C, preferably for 5 to 20 hours.
  • the natural ageing preferably comprises a step of ageing at room temperature during 1 to 10 days.
  • the aluminium alloy product is aged to a temper selected from the group comprising T3, T351 , T39, T6, T651 , and T87.
  • the aluminium alloy product is processed to fuselage sheet, preferably to fuselage sheet having a thickness of less then 30 mm.
  • the aluminium alloy product is processed to lower wing plate.
  • the aluminium alloy product is processed to upper wing plate.
  • the aluminium alloy product is processed to an extruded product.
  • the aluminium alloy product is processed to a forged product. In yet another embodiment the aluminium alloy product is processed to a thin plate having a thickness in the range of 15 to 40 mm.
  • the aluminium alloy product is processed to a thick plate having a thickness up to 300 mm.
  • Fig. 1 shows a Cr-Ti diagram setting out the Cr-Ti range for the invention together with narrower preferred ranges.
  • Fig. 1 shows schematically the ranges for the Cr and Ti content for the alloy according to the invention. The broadest range is identified by a rectangular box with angular points A, B, C, D.
  • Fig. 1 also shows schematically a preferred range of a balanced content of both Cr and Ti.
  • the broadest range thereof is identified by a quadrangular box with angular points E, F, G, H.
  • the point P indicates the Cr and Ti content of a sample of an alloy according to the invention which was used for testing (also referred to as Alloy 3 in the following examples).
  • alloys 1 and 2 indicate the Cr and Ti content of two comparative alloys, also used for testing and also referred to as alloys 1 and 2. Alloys 1 and 2 fall outside the invention.
  • Alloy 2 has, with the exception of the Cr and Ti content, the same chemical composition as Alloy 3 according to the invention.
  • Alloy 1 has a chemical composition typical for a conventional AA2024 alloy.
  • the alloys listed in Table 1 were processed as follows: Casting an ingot;
  • Alloy 1 homogenising the ingot at a heating rate of 30 °C/h to 465 0 C, soaking at that temperature for 2 hours followed by further heating at a rate of 15 °C/h to 495 0 C and soaking at that temperature for 24 hours followed by air cooling to room temperature.
  • Quenching the cold rolled plate by either direct water quenching or quenching in water after holding 10 sec. in still air.
  • Stretching and ageing the cold rolled plate by either: o Stretching and natural ageing for 5 days at room temperature to T3x tempers (viz. T3, T351 , and T39); or o Stretching and artificial ageing for 12 hours at 175 0 C to T6x and T8x tempers (viz. T6, T651 , 187).
  • Table 2 shows that a balanced addition of Cr and Ti according to an embodiment of the invention gives rise to outstanding intergranular corrosion free properties in the T3x tempers with a markedly lower pit depth compared with the other alloys.
  • Figs. 2a, 2b, 3a and 3b show micrographs of a cross section of a sample of an alloy according to the invention in T3 temper and of a comparative alloy after corrosion testing.
  • Fig. 2a shows a micrograph of a cross section of a sample of comparative alloy 1 (Ref. AA2024) in T3 temper after corrosion testing.
  • the micrograph clearly shows pitting corrosion and intergranular corrosion to a depth of more than 150 ⁇ m.
  • Fig. 2b shows a micrograph of a cross section of a sample of an alloy according to the invention (alloy 3) also in T3 temper after corrosion testing. The samples show only slight pitting, with a maximum depth of 60 ⁇ m and no intergranular corrosion.
  • Figs. 3a, 3b show micrographs of a cross section of sample of an alloy according to the invention in T6 temper and of a comparative alloy after corrosion testing.
  • Fig. 3a shows a micrograph of a cross section of a sample of a comparative alloy 1 (Ref. AA2024) in T6 temper after corrosion testing.
  • the micrograph clearly shows local intergranular corrosion, extending to a depth of about 220 ⁇ m.
  • Fig. 3b shows a micrograph of a cross section of a sample of an alloy according to the invention (alloy 3) also in T6 temper after corrosion testing.
  • the sample exhibits pitting with only slight intergranular corrosion to a depth of less than 160 ⁇ m.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Extrusion Of Metal (AREA)
  • Metal Rolling (AREA)
EP06818278.1A 2005-10-25 2006-10-24 Al-cu-mg- legierung für luftfahrtanwendung Active EP1945825B1 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP06818278.1A EP1945825B1 (de) 2005-10-25 2006-10-24 Al-cu-mg- legierung für luftfahrtanwendung

Applications Claiming Priority (3)

Application Number Priority Date Filing Date Title
EP05077448 2005-10-25
EP06818278.1A EP1945825B1 (de) 2005-10-25 2006-10-24 Al-cu-mg- legierung für luftfahrtanwendung
PCT/EP2006/010216 WO2007048565A1 (en) 2005-10-25 2006-10-24 Al-cu-mg alloy suitable for aerospace application

Publications (2)

Publication Number Publication Date
EP1945825A1 true EP1945825A1 (de) 2008-07-23
EP1945825B1 EP1945825B1 (de) 2014-06-25

Family

ID=36572409

Family Applications (1)

Application Number Title Priority Date Filing Date
EP06818278.1A Active EP1945825B1 (de) 2005-10-25 2006-10-24 Al-cu-mg- legierung für luftfahrtanwendung

Country Status (6)

Country Link
EP (1) EP1945825B1 (de)
CN (1) CN101297054A (de)
BR (1) BRPI0617699A2 (de)
CA (1) CA2627070C (de)
RU (1) RU2418876C2 (de)
WO (1) WO2007048565A1 (de)

Cited By (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2020200869A1 (en) * 2019-04-03 2020-10-08 Aleris Rolled Products Germany Gmbh Method of producing a high-energy hydroformed structure from a 2xxx-series alloy

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CN101649433B (zh) * 2009-07-10 2012-11-21 西南铝业（集团）有限责任公司 一种铝合金板材的加工方法
CN103168111B (zh) * 2010-10-08 2015-07-29 美铝公司 改进的2xxx铝合金及其生产方法
ES2565482T3 (es) * 2011-08-17 2016-04-05 Otto Fuchs Kg Aleación de Al-Cu-Mg-Ag resistente al calor, así como procedimiento para la fabricación de un producto semiacabado o producto a partir de una aleación de aluminio de este tipo
CN102925829A (zh) * 2012-11-22 2013-02-13 哈尔滨工业大学 Al-Cu-Mg-Si系铝合金薄壁环状构件的热处理方法
JP6057855B2 (ja) * 2013-07-31 2017-01-11 株式会社神戸製鋼所 切削用アルミニウム合金押出材
RU2573164C1 (ru) * 2014-10-02 2016-01-20 Федеральное государственное автономное образовательное учреждение высшего профессионального образования "Белгородский государственный национальный исследовательский университет" (НИУ "БелГУ") Высокопрочный деформируемый сплав на основе алюминия
CN105002408A (zh) * 2015-07-12 2015-10-28 河北钢研德凯科技有限公司 一种优质高强铸造铝合金材料及制备方法
CN105239029B (zh) * 2015-10-23 2017-12-08 中铝材料应用研究院有限公司 控制Al‑Cu‑Mg‑Mn合金中含Mn相均匀弥散析出的热处理方法
CN105908028B (zh) * 2016-06-16 2018-02-27 江苏大学 一种设计高淬透性高强度铝合金主要成分的方法
CN110114498A (zh) * 2016-10-24 2019-08-09 形状集团 用于生产车辆零件的多阶段铝合金形成与热加工方法
CN108118273B (zh) * 2017-12-11 2019-11-12 中南大学 一种改善铝合金抗腐蚀性能的方法
CN109136697B (zh) * 2018-08-28 2020-12-22 兰州飞行控制有限责任公司 一种高强度铝铜系铝合金
US20220002853A1 (en) * 2018-11-12 2022-01-06 Airbus Sas Method of producing a high-energy hydroformed structure from a 7xxx-series alloy
CN110724866A (zh) * 2019-11-28 2020-01-24 西南铝业（集团）有限责任公司 一种2014铝合金航空精密轮毂模锻件的无锆毛坯
CN111020321B (zh) * 2019-12-11 2021-09-14 兰州飞行控制有限责任公司 一种适于锻造加工的Al-Cu系铸造合金及其制备方法
CN111101038A (zh) * 2019-12-20 2020-05-05 山东南山铝业股份有限公司 一种多元耐热铝合金及其制备方法
FR3111143B1 (fr) * 2020-06-04 2022-11-18 Constellium Issoire Produits en alliage aluminium cuivre magnésium performants à haute température
CN112281033B (zh) * 2020-09-25 2021-09-28 中南大学 一种同时提高铝铜镁合金油井管耐腐蚀和耐热性的方法
CN113897524A (zh) * 2021-10-09 2022-01-07 山东创新精密科技有限公司 一种电导率均匀度高的铝合金及其制备方法和应用
CN114134376A (zh) * 2021-12-08 2022-03-04 无锡市世达精密焊管制造有限公司 一种Mg-Cu铝合金及其制备方法
CN115821131B (zh) * 2022-12-05 2024-05-14 山东南山铝业股份有限公司 一种低疲劳裂纹扩展速率2系铝合金型材及其制造方法
CN115927936B (zh) * 2022-12-22 2023-06-09 北京机科国创轻量化科学研究院有限公司 一种高强韧铝合金及其制备方法
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Also Published As

Publication number Publication date
RU2418876C2 (ru) 2011-05-20
EP1945825B1 (de) 2014-06-25
CA2627070A1 (en) 2007-05-03
RU2008115928A (ru) 2009-10-27
WO2007048565A1 (en) 2007-05-03
CN101297054A (zh) 2008-10-29
CA2627070C (en) 2014-07-29
BRPI0617699A2 (pt) 2011-08-02

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