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WO2005045080A1 - Alliage d'alminium - Google Patents

Alliage d'alminium Download PDF

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Publication number
WO2005045080A1
WO2005045080A1 PCT/AT2004/000397 AT2004000397W WO2005045080A1 WO 2005045080 A1 WO2005045080 A1 WO 2005045080A1 AT 2004000397 W AT2004000397 W AT 2004000397W WO 2005045080 A1 WO2005045080 A1 WO 2005045080A1
Authority
WO
WIPO (PCT)
Prior art keywords
weight
aluminum alloy
alloy according
less
manganese
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.)
Ceased
Application number
PCT/AT2004/000397
Other languages
German (de)
English (en)
Inventor
Anja Hölzl
Valentin Konkevich
Helmut Kaufmann
Peter Uggowitzer
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.)
LKR Leichtmetallkompetenzzentrum Ranshofen GmbH
Original Assignee
LKR Leichtmetallkompetenzzentrum Ranshofen 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
Application filed by LKR Leichtmetallkompetenzzentrum Ranshofen GmbH filed Critical LKR Leichtmetallkompetenzzentrum Ranshofen GmbH
Publication of WO2005045080A1 publication Critical patent/WO2005045080A1/fr
Anticipated expiration legal-status Critical
Ceased legal-status Critical Current

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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

Definitions

  • the invention relates to an aluminum alloy.
  • the invention further comprises a method for producing starting material for components made of an aluminum alloy that can be produced by soldering.
  • Aluminum-manganese alloys have been used for many years for components of heat exchangers or the like components which are used at temperatures of up to 400 ° C. These alloys, also known as “3000 alloys" in technical jargon, are characterized by good thermal conductivity and consistently high corrosion resistance.
  • aluminum-manganese alloys continue to have good formability, and castings or primary materials made from such alloys can generally be easily formed into sheets, which in turn are processed into various objects such as heat exchangers.
  • aluminum-manganese alloy sheets can be plated on one or both sides with a layer which has a lower melting point than the aluminum-manganese alloy representing a base material.
  • Clad sheet metal parts can be placed in the area of the
  • Plating layers, subsequent melting of the plating layers and subsequent cooling of the sheet metal parts are bonded together. Since on the one hand mostly aluminum-silicon If alloys with a eutectic composition are used, i.e. alloys with a melting point of approx. 570 ° C and, on the other hand, melt aluminum-manganese alloys at temperatures above approx. 615 ° C, a material connection can be ensured at 600 "C without the base material melting ,
  • Corrosion resistance is of no use if a component is mechanical
  • tensile strength values of Rm ⁇ 50 MPa are common values for parts made of aluminum-manganese alloys.
  • precipitation hardening can be achieved by soldering: Due to the high thermal conductivity of aluminum-manganese alloys, the base material quickly heats up to approx. 600 ° C and this temperature is sufficient to dissolve copper, which is why at one subsequent increased cooling or quenching of the soldered parts and subsequent aging, the aforementioned Al-Mn-Cu phases are eliminated.
  • the tensile strengths Rm achieved with such an alloy after brazing are limited to 75 MPa.
  • the object of the invention is to provide an aluminum-manganese alloy which, in addition to good formability and corrosion resistance, can be tempered to high mechanical parameters and which is particularly suitable for use as a base material in clad sheets for the production of heat exchangers.
  • alloys according to the invention After heat treatment at 600 ° C, followed by aging, alloys according to the invention have high mechanical characteristics, which is why they are particularly suitable as base materials for clad sheets, which are used for the production of heat exchangers and which are hardened by means of a soldering process, optionally with subsequent hot aging become.
  • Manganese (Mn) In the content range from 0.6% to 1.5% by weight, manganese contributes significantly to corrosion resistance and strength, whereby the contribution of manganese to strength can be seen in connection with a given iron content.
  • Manganese is generally not very soluble in equilibrium in ⁇ -aluminum, but remains in solution when a poured melt cools down rapidly. However, the presence of iron in the alloy according to the invention counteracts this oversaturation with the formation of strength-increasing Al ⁇ CMnFe) precipitates.
  • Preferred levels of manganese are in the range of 0.8% to 1.1% by weight because the best mechanical properties can be observed in these ranges.
  • Scandium In an alloy according to the invention, scandium is mandatory in contents of 0.05% by weight to 0.5% by weight. Scandium works in several ways: First, when scandium and zircon are present, A Sc, AI 3 Zr and possibly mixed phases form during hardening, which contribute significantly to the material strength. Secondly, scandium has a grain-refining effect and thus further increases the strength. Finally, the alloying of scandium can also shift the recrystallization temperature to significantly higher temperatures.
  • Zirconium mainly forms an increase in strength through the formation of zirconium-containing precipitates such as A ⁇ Zr0 and has a positive effect in this regard in a content range from 0.025% by weight to 0.25% by weight. It is particularly favorable if the weight ratio scandium to zircon is more than 2 and less than 4, preferably more than 2.6 and less than 3.4. With such a ratio, there is mainly the formation of Al 3 (Sr ⁇ -x Zr x ), since zircon - with the weight ratios mentioned - can be completely incorporated into the Al 3 Sc crystal lattice.
  • An AI 3 (Sr ⁇ . ⁇ Zr x ) phase is preferred in terms of elimination kinetics, because this phase tends to coagulate less in comparison with AI 3 Sc or AI 3 Zr and therefore favors a homogeneous microstructure.
  • Iron (Fe) In the alloy according to the invention, iron is mandatory and causes an excretion of Al ⁇ (MnFe.) In the intended contents.
  • An upper limit of 0.90% by weight of iron results due to disadvantageous forming properties at higher contents. For example, undesired cracking can occur when rolling if the iron content is greater than 0.90% by weight.
  • iron contents of 0.15% by weight to 0.7% by weight, preferably 0.25% by weight to 0.55% by weight, have proven successful.
  • Chromium contents of up to 0.25% by weight have a favorable effect on the strength of alloys according to the invention. At levels higher than 0.25% by weight, undesirable coarse intermetallic phases can form, which is why this chromium content represents an upper limit.
  • the chromium content should be at least 0.0125% by weight, it being particularly preferred if the weight ratio of zirconium to chromium is more than 0.5 and less than 2.5 and the weight ratio of scandium to zirconium is more than 2 and less than 4. According to current considerations and findings, fine precipitates of an AlmSc n Zr p Cr q phase are formed in this case.
  • Silicon can cause fine Al (MnFe) Si phases to form in aluminum-manganese alloys, but at higher contents, in particular higher than 0.7% by weight, hot cracking is frequently observed in continuous casting. It is therefore preferred to set the silicon content to less than 0.3% by weight, particularly preferably to less than 0.1% by weight, of silicon.
  • Magnesium has a strength-increasing effect in an alloy according to the invention and can be provided in contents of up to 1.5% by weight.
  • a magnesium concentration in the material it is preferred to provide magnesium at a content of at least 0.5% by weight, because then the amazing effect can be observed that the yield strength R p o, 2 is higher at 150 ° C, i.e. in the range of typical use temperatures than at room temperature. A plausible explanation for this effect is given by the formation of Mg-containing precipitates at these temperatures.
  • a maximum magnesium content it is preferred to provide magnesium with a maximum of 1.05% by weight because the tensile strength decreases at higher contents.
  • Copper can be present in contents of up to 1.5% by weight and can contribute to increasing the strength by forming ternary Al-Mn-Cu phases. For reasons of corrosion chemistry, however, it is preferred to limit the copper content to less than 0.15% by weight, preferably less than 0.10% by weight.
  • Zinc levels of up to 1.5% by weight can be present without a significant influence on the mechanical properties. However, lower contents of less than 0.5%, preferably less than 0.10% zinc are preferred.
  • titanium can be provided in an alloy according to the invention in a content of up to 0.10% by weight. It has proven to be advantageous to use titanium with contents of 0.01% by weight to 0.05% by weight: grain refinement effects are less pronounced below 0.01% by weight, and the grain refinement effect of titanium decreases above 0.05% by weight.
  • This goal is achieved in that a melt is created from an aluminum alloy according to the invention in a method of the type mentioned at the outset, after which the melt is poured into a wide-flat starting material and allowed to solidify.
  • the advantages achieved in terms of the process can be seen in particular in that, by casting an alloy according to the invention in wide-flat primary material, an advantageous cast structure with small size precipitates is achieved and the sheets produced from such panels or panel-shaped primary materials have excellent mechanical properties.
  • the preliminary material thus created can expediently be formed into a semi-finished product.
  • the process is advantageously carried out in such a way that the primary material is formed by hot rolling and then cold rolling. In this way, the primary material can be processed in a simple manner into sheets with a small sheet thickness.
  • Exemplary alloys A, B, C and D with chemical compositions according to Table 1 are cast in 2 cm by 23 cm by 23 cm plates. Furthermore, round bolts with a diameter of 7 cm and a height of 17 cm are created from these alloys.
  • Table 1 Chemical composition of alloys A, B, C and D according to the invention (all data in percent by weight)
  • the cast plates and round bolts are then rolled at a temperature of 550 ° C to 580 ° C to a thickness of 1 cm.
  • Table 2 shows the hardness values determined on rolled plates before and after a heat treatment consisting of solution annealing at a temperature of 630 ° C. to 635 ° C. for 10 minutes, a subsequent quenching to room temperature and a subsequent heat aging at 300 ° C. for 300 minutes , It can be seen that alloy D has the greatest hardness in the hardened state (the hardness values in Table 2 and also below are Brinell hardnesses 2.5 / 62.5 / 16).
  • Table 4 shows the yield strength (R p o, 2 ).
  • the tensile strength (R m ), the elongation at break (A5) and the constriction (Z) for tempered sheets of alloys A, B, C and D according to the invention are given in Table 1.
  • Table 4 The values given in Table 4 correspond to test pieces which were made from sheet metal which had been annealed at 600 ° C. to 605 ° C. for 10 minutes, then quenched to room temperature and then aged at 300 ° C. for 300 minutes.
  • Table 4 Yield strength R p o, 2 , tensile strength R m , elongation at break A 5 and constriction Z for sheets annealed at 600-605 ° C (L ... values in the rolling direction, Q ... values in the transverse direction)
  • Table 4 shows, inter alia, that sheets made from the alloy according to the invention can have a high tensile strength of over 100 MPa even at 300 ° C.
  • alloys A creep tests on sheets made from plate-shaped or broad-flat primary material, which were subjected to a heat treatment comprising solution annealing at 600 ° C. for 10 minutes, subsequent quenching and hot aging at 300 ° C. , B, C and D after 200 hours of tensile stress of 100 MPa at 150 ° C elongation values ⁇ of less than 0.3%, both lengthways and crossways to the rolling direction. Sheets made of alloys B, C and D showed particularly low elongation values ⁇ of less than 0.15%.
  • an alloy or sheet according to the invention can be subjected to the same alternative heat treatment method. It is thus possible to hot-roll broad-flat stock material in several passes at a temperature of over 200 ° C and then cold-roll it at ambient temperature, and finally to subject the sheets thus produced to soft annealing at 350 ° C for 90 minutes. Sheets made and treated accordingly from alloys B, C and D showed yield strength values R p0 , 2 of more than 280 MPa and tensile strength values R m of more than 300 MPa.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
  • Metal Rolling (AREA)

Abstract

L'objectif de l'invention est de produire un alliage aluminium/ manganèse, comprenant de bonnes caractéristiques mécaniques, ainsi qu'une bonne plasticité et une bonne résistance à la corrosion, et qui convient particulièrement comme matière de base pour des feuilles plaquées dans la production d'échangeurs thermiques. Selon l'invention, un alliage d'aluminium est utilisé, comprenant en pourcentage en poids : 0.6 % à 1,5 % de manganèse, 0.05 % à 0,5 % de scandium, 0.025 % à 0.25 % de zircon, 0.10 % à 0,90 % de fer, jusqu'à 0.25 % de chrome, jusqu'à 0.7 % de silicium, jusqu'à 1.5 % de magnésium, jusqu'à 1.5 % de cuivre, jusqu'à 1.5 % de zinc, jusqu'à 0.10 % de titane, le reste étant composé d'aluminium et des impuretés qui ne peuvent pas être éliminées de la production. L'invention concerne également la production de matériaux de démarrage pour des composants fabriqués à partir d'alliages d'aluminium, produits par soudage, un mélange avec une composition correspondant à l'alliage d'aluminium ci-dessus étant produite, ledit mélange étant moulé de manière à créer un matériau de départ large et plat et il est conçu pour durcir. Des produits semi-finis de grande qualité peuvent être produits grâce audit procédé.
PCT/AT2004/000397 2003-11-10 2004-11-10 Alliage d'alminium Ceased WO2005045080A1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
AT0180403A AT413035B (de) 2003-11-10 2003-11-10 Aluminiumlegierung
ATA1804/2003 2003-11-10

Publications (1)

Publication Number Publication Date
WO2005045080A1 true WO2005045080A1 (fr) 2005-05-19

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Country Link
AT (1) AT413035B (fr)
WO (1) WO2005045080A1 (fr)

Cited By (29)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1728881A3 (fr) * 2005-05-31 2007-02-21 United Technologies Corporation Alliages d' aluminium pour utilisation à haute temperature
RU2384637C1 (ru) * 2008-07-21 2010-03-20 Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") Деформируемый термически неупрочняемый сплав на основе алюминия
RU2384636C1 (ru) * 2008-07-21 2010-03-20 Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") Деформируемый термически неупрочняемый сплав на основе алюминия
US7871477B2 (en) 2008-04-18 2011-01-18 United Technologies Corporation High strength L12 aluminum alloys
US7875131B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation L12 strengthened amorphous aluminum alloys
US7875133B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation Heat treatable L12 aluminum alloys
US7879162B2 (en) 2008-04-18 2011-02-01 United Technologies Corporation High strength aluminum alloys with L12 precipitates
US7909947B2 (en) 2008-04-18 2011-03-22 United Technologies Corporation High strength L12 aluminum alloys
RU2425165C1 (ru) * 2010-03-15 2011-07-27 Государственное образовательное учреждение высшего профессионального образования "Белгородский государственный университет" Жаропрочный деформируемый сплав на основе алюминия и изделие, выполненное из него
US8002912B2 (en) 2008-04-18 2011-08-23 United Technologies Corporation High strength L12 aluminum alloys
US8017072B2 (en) 2008-04-18 2011-09-13 United Technologies Corporation Dispersion strengthened L12 aluminum alloys
RU2446222C1 (ru) * 2010-10-29 2012-03-27 Федеральное государственное образовательное учреждение высшего профессионального образования "Национальный исследовательский технологический университет "МИСиС" Термостойкий сплав на основе алюминия и способ получения из него деформированных полуфабрикатов
US8409496B2 (en) 2009-09-14 2013-04-02 United Technologies Corporation Superplastic forming high strength L12 aluminum alloys
US8409373B2 (en) 2008-04-18 2013-04-02 United Technologies Corporation L12 aluminum alloys with bimodal and trimodal distribution
US8409497B2 (en) 2009-10-16 2013-04-02 United Technologies Corporation Hot and cold rolling high strength L12 aluminum alloys
US8728389B2 (en) 2009-09-01 2014-05-20 United Technologies Corporation Fabrication of L12 aluminum alloy tanks and other vessels by roll forming, spin forming, and friction stir welding
US8778098B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Method for producing high strength aluminum alloy powder containing L12 intermetallic dispersoids
US8778099B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Conversion process for heat treatable L12 aluminum alloys
CN104878254A (zh) * 2015-05-29 2015-09-02 柳州普亚贸易有限公司 耐冲击门窗用铝合金
US9127334B2 (en) 2009-05-07 2015-09-08 United Technologies Corporation Direct forging and rolling of L12 aluminum alloys for armor applications
US9194027B2 (en) 2009-10-14 2015-11-24 United Technologies Corporation Method of forming high strength aluminum alloy parts containing L12 intermetallic dispersoids by ring rolling
CN106282696A (zh) * 2015-05-19 2017-01-04 沈阳万龙源冶金新材料科技有限公司 一种高强高韧铝合金
EP3362581A4 (fr) * 2015-10-14 2019-04-17 Nanoal LLC Alliages de zirconium-aluminium-fer
RU2716566C1 (ru) * 2019-12-18 2020-03-12 Федеральное государственное автономное образовательное учреждение высшего образования "Национальный исследовательский технологический университет "МИСиС" Способ получения деформированных полуфабрикатов из алюминиево-кальциевого композиционного сплава
WO2020064291A1 (fr) * 2018-09-24 2020-04-02 Aleris Rolled Products Germany Gmbh Matériau de tôle à ailettes en alliage d'aluminium
EP3592874A4 (fr) * 2017-03-08 2020-10-21 Nanoal LLC Alliages d'aluminium de série 3000 à haute performance
US11471984B2 (en) 2018-06-28 2022-10-18 Scandium International Mining Corporation Control of recrystallization in cold-rolled AlMn(Mg)ScZr sheets for brazing applications
CN118186267A (zh) * 2024-05-17 2024-06-14 辽宁铝镁锌金属涂层有限公司 一种高耐蚀热浸镀铝合金钢件及其生产方法
WO2025200455A1 (fr) * 2024-03-29 2025-10-02 深圳星富丽实业发展有限责任公司 Matériau d'alliage aluminium-fer-nickel-silicium-magnésium-titane de coulée et son procédé de préparation

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CN117488141B (zh) * 2023-09-25 2024-07-26 安徽广银铝业有限公司 一种铝锰合金动力电池壳体及其加工方法

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US7875132B2 (en) 2005-05-31 2011-01-25 United Technologies Corporation High temperature aluminum alloys
EP1728881A3 (fr) * 2005-05-31 2007-02-21 United Technologies Corporation Alliages d' aluminium pour utilisation à haute temperature
US7883590B1 (en) 2008-04-18 2011-02-08 United Technologies Corporation Heat treatable L12 aluminum alloys
US8002912B2 (en) 2008-04-18 2011-08-23 United Technologies Corporation High strength L12 aluminum alloys
US8409373B2 (en) 2008-04-18 2013-04-02 United Technologies Corporation L12 aluminum alloys with bimodal and trimodal distribution
US7875131B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation L12 strengthened amorphous aluminum alloys
US7875133B2 (en) 2008-04-18 2011-01-25 United Technologies Corporation Heat treatable L12 aluminum alloys
US7879162B2 (en) 2008-04-18 2011-02-01 United Technologies Corporation High strength aluminum alloys with L12 precipitates
US8017072B2 (en) 2008-04-18 2011-09-13 United Technologies Corporation Dispersion strengthened L12 aluminum alloys
US7909947B2 (en) 2008-04-18 2011-03-22 United Technologies Corporation High strength L12 aluminum alloys
US7871477B2 (en) 2008-04-18 2011-01-18 United Technologies Corporation High strength L12 aluminum alloys
RU2384636C1 (ru) * 2008-07-21 2010-03-20 Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") Деформируемый термически неупрочняемый сплав на основе алюминия
RU2384637C1 (ru) * 2008-07-21 2010-03-20 Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") Деформируемый термически неупрочняемый сплав на основе алюминия
US8778099B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Conversion process for heat treatable L12 aluminum alloys
US8778098B2 (en) 2008-12-09 2014-07-15 United Technologies Corporation Method for producing high strength aluminum alloy powder containing L12 intermetallic dispersoids
US9127334B2 (en) 2009-05-07 2015-09-08 United Technologies Corporation Direct forging and rolling of L12 aluminum alloys for armor applications
US8728389B2 (en) 2009-09-01 2014-05-20 United Technologies Corporation Fabrication of L12 aluminum alloy tanks and other vessels by roll forming, spin forming, and friction stir welding
US8409496B2 (en) 2009-09-14 2013-04-02 United Technologies Corporation Superplastic forming high strength L12 aluminum alloys
US9194027B2 (en) 2009-10-14 2015-11-24 United Technologies Corporation Method of forming high strength aluminum alloy parts containing L12 intermetallic dispersoids by ring rolling
US8409497B2 (en) 2009-10-16 2013-04-02 United Technologies Corporation Hot and cold rolling high strength L12 aluminum alloys
RU2425165C1 (ru) * 2010-03-15 2011-07-27 Государственное образовательное учреждение высшего профессионального образования "Белгородский государственный университет" Жаропрочный деформируемый сплав на основе алюминия и изделие, выполненное из него
RU2446222C1 (ru) * 2010-10-29 2012-03-27 Федеральное государственное образовательное учреждение высшего профессионального образования "Национальный исследовательский технологический университет "МИСиС" Термостойкий сплав на основе алюминия и способ получения из него деформированных полуфабрикатов
CN106282696A (zh) * 2015-05-19 2017-01-04 沈阳万龙源冶金新材料科技有限公司 一种高强高韧铝合金
CN104878254A (zh) * 2015-05-29 2015-09-02 柳州普亚贸易有限公司 耐冲击门窗用铝合金
EP3362581A4 (fr) * 2015-10-14 2019-04-17 Nanoal LLC Alliages de zirconium-aluminium-fer
US10633725B2 (en) 2015-10-14 2020-04-28 NaneAL LLC Aluminum-iron-zirconium alloys
EP3592874A4 (fr) * 2017-03-08 2020-10-21 Nanoal LLC Alliages d'aluminium de série 3000 à haute performance
US12018354B2 (en) 2017-03-08 2024-06-25 NanoAL LLC High-performance 3000-series aluminum alloys
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RU2716566C1 (ru) * 2019-12-18 2020-03-12 Федеральное государственное автономное образовательное учреждение высшего образования "Национальный исследовательский технологический университет "МИСиС" Способ получения деформированных полуфабрикатов из алюминиево-кальциевого композиционного сплава
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