EP1441041A1 - Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit - Google Patents

Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit Download PDF

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Publication number
EP1441041A1
EP1441041A1 EP03405013A EP03405013A EP1441041A1 EP 1441041 A1 EP1441041 A1 EP 1441041A1 EP 03405013 A EP03405013 A EP 03405013A EP 03405013 A EP03405013 A EP 03405013A EP 1441041 A1 EP1441041 A1 EP 1441041A1
Authority
EP
European Patent Office
Prior art keywords
temperature
max
weight
bars
aluminum 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.)
Withdrawn
Application number
EP03405013A
Other languages
German (de)
English (en)
French (fr)
Inventor
Günther Höllrigl
Christophe Jaquerod
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.)
3A Composites International AG
Original Assignee
Alcan Technology and Management Ltd
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 Alcan Technology and Management Ltd filed Critical Alcan Technology and Management Ltd
Priority to EP03405013A priority Critical patent/EP1441041A1/de
Priority to ES03789376T priority patent/ES2290544T3/es
Priority to RU2005125727/02A priority patent/RU2351674C2/ru
Priority to PL376309A priority patent/PL203780B1/pl
Priority to US10/541,788 priority patent/US20060096676A1/en
Priority to AU2003293963A priority patent/AU2003293963A1/en
Priority to CA2513333A priority patent/CA2513333C/en
Priority to PT03789376T priority patent/PT1587965E/pt
Priority to AT03789376T priority patent/ATE367456T1/de
Priority to EP03789376A priority patent/EP1587965B1/de
Priority to DK03789376T priority patent/DK1587965T3/da
Priority to PCT/EP2003/014696 priority patent/WO2004063407A1/de
Priority to SI200330959T priority patent/SI1587965T1/sl
Priority to DE50307736T priority patent/DE50307736D1/de
Priority to TW092136857A priority patent/TWI291993B/zh
Publication of EP1441041A1 publication Critical patent/EP1441041A1/de
Priority to HR20050704A priority patent/HRP20050704B1/xx
Priority to NO20053832A priority patent/NO340750B1/no
Priority to US12/402,966 priority patent/US7901522B2/en
Withdrawn legal-status Critical Current

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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
    • C22C21/10—Alloys based on aluminium with zinc as the next major constituent
    • 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
    • C22F1/053—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 zinc as the next major constituent
    • 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
    • C22F1/057—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 copper as the next major constituent

Definitions

  • the invention relates to an aluminum alloy with high strength and low Quench.
  • a method is also within the scope of the invention for the production of thick plates made of aluminum alloy.
  • a major disadvantage of the aluminum alloys used today for mold making is their high sensitivity to quenching. So that the ingot or Sheets in hot curing that required for plastic injection molds Reach the strength level, the cooling rate of the homogenization or solution annealing temperature with increasing plate thickness increase. Due to the high temperature gradients that occur between the surface and the core of the ingot or plate the harmful residual stresses, so for this reason alone a further increase in the cooling rate and ultimately that achievable strength levels are limited.
  • the invention has for its object one for the production of thick Sheets of high strength suitable aluminum alloy with low To provide quench sensitivity.
  • Another object of the invention is to provide a suitable method with which the aluminum alloy to thick plates with sufficiently high Strength can be processed over the entire board thickness.
  • An aluminum alloy is used to achieve the object according to the invention 4.6 to 5.2% by weight Zn 2.6 to 3.0% by weight mg 0.1 to 0.2% by weight Cu 0.05 to 0.2% by weight Zr Max. 0.05% by weight Mn Max. 0.05% by weight Cr Max. 0.15% by weight Fe Max. 0.15% by weight Si Max. 0.10% by weight Ti and aluminum as the rest with production-related impurities, individually max. 0.05% by weight, total max. 0.15% by weight.
  • the composition of the alloy is selected such that it has a very low sensitivity to quenching and is nevertheless extremely good has a high level of strength. Thick cross sections can therefore with forced air cooling and through precipitation hardening to a high level Strength level are brought.
  • an isotropic distribution of the residual stresses in the cross section of the plate is to be aimed for.
  • the grain size and the shape of the grain in the plate are of importance for the reduction of the internal stresses. The finer and more uniform the crystals are, the better the internal stresses in the cross-section of the plate can balance.
  • the grain boundaries act as sinks for dislocations when local stress peaks are reduced.
  • the addition of zirconium can achieve a fine grain structure in the plate by selecting the rate at which the ingots heat up to the homogenization or solution annealing temperature in such a way that the distribution of submicron precipitates of Al 3 Zr in the structure is as homogeneous as possible arises.
  • the ingot is preferably cooled from the homogenization temperature from 470 to 490 ° C to the intermediate temperature of 400 to 410 ° C at rest Air.
  • the cooling of the bars from the intermediate temperature of 400 to 410 ° C should on the one hand, so quickly that the loss of strength is as low as possible. On the other hand, the cooling rate must not be too high, either otherwise excessive internal stresses can be built up.
  • the cooling of the bars from the intermediate temperature of 400 to 410 ° C on a temperature of less than 100 ° C is preferably in moving air (forced air cooling) or in a water / air spray.
  • the bar thickness must also be taken into account when choosing the cooling conditions become. However, it is within the scope of professional action for a given ingot format based on the optimal cooling conditions easier attempts to determine.
  • the low heating rate in the temperature range between 170 and 410 ° C. when the bars are heated to the homogenization temperature is an essential feature of the process according to the invention.
  • the AlZnMg equilibrium phase (T phase) is stable.
  • the slow passage through the heterogenization interval leads to a finely dispersed separation of the T phase, the phase interfaces of the separated particles of the T phase forming preferred nucleation sites for the precipitation of Al 3 Zr particles starting at a temperature of about 350 ° C.
  • the ingot When the ingot is further heated to the homogenization temperature, the previously separated particles of the T phase dissolve and what remains is an even distribution of the fine, submicron Al 3 Zr precipitates, which are preferably due to the original particle boundaries of the T phase and to subcom boundaries and so that there is a homogeneous distribution.
  • These fine Al 3 Zr particles cause a strong growth inhibition in the recrystallization of the plates in solution annealing as well as in the homogenization annealing of cast ingots, and the desired isotropic grain structure in the ingot results.
  • the grain-refining additional element Zr is thus optimally used.
  • Another essential feature of the method according to the invention is that combined homogenization and solution annealing with subsequent two-stage cooling, whereas in the usual processes according to the state the technology to achieve an acceptable level in the middle of the bar Strength a separate solution heat treatment with subsequent quenching high cooling rate is required.
  • cooling in moving air or “forced air cooling” is understood here to mean an air cooling which is usually supported by fans and which leads to a heat transfer coefficient on the bar surface of approximately 40 W / m 2 K. Cooling in a water / air spray leads to a somewhat higher heat transfer coefficient on the bar surface.
  • the alloy according to the invention has a low sensitivity to quenching on.
  • the two-stage cooling of the homogenization temperature to room temperature is particularly advantageous to achieve a structure with low residual stresses.
  • Heat curing to the heat treatment state is particularly preferred T76.
  • the field of application of the alloy according to the invention and of this The thick plates produced result from the above Spectrum of properties.
  • the plates are particularly suitable for mold making, i.e. for the production of plastic injection molds, but also in general for machine, tool and mold making.
  • the ingot was placed on a bar within 30 hours Temperature of 480 ° C heated, taking care that the heating rate in the range between 170 and 410 ° C less than 20 ° C / h scam.
  • the homogenization of the ingot to compensate for the solidification Crystal segregation was carried out by holding the ingot for 12 hours 480 ° C.
  • the homogenized ingot was in a first stage in still air from the homogenization temperature to an intermediate temperature of 400 ° C and then cooled in a second stage with fans from 400 ° C to 100 ° C. The further cooling to room temperature again took place at rest Air.
  • the ingot was stored for 8 hours after 14 days of storage at room temperature at 95 ° C and then for 18 hours at 155 ° C to the over-hardened state T76 hardened warm.
  • FIG. 2 the temperature-time curves for a fan cooling are calculated for the surface (O) and the core (K) of an ingot with a cross section of 440 ⁇ 900 mm, and in FIG. 3 the gradients between the temperature T derived therefrom K in the ingot core and the temperature T o on the ingot surface.
  • FIGS. 4 and 5 show the corresponding curves for an ingot with a cross section of 1000 x 1200 mm. The results show that bars produced with the method according to the invention with a thickness of up to 1000 mm are still likely to meet the mechanical strength requirements placed on plates for the production of plastic injection molds.

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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)
  • Continuous Casting (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
  • Metal Rolling (AREA)
  • Investigating Or Analyzing Materials By The Use Of Fluid Adsorption Or Reactions (AREA)
  • Manufacture Of Alloys Or Alloy Compounds (AREA)
  • Laminated Bodies (AREA)
  • Contacts (AREA)
  • Conductive Materials (AREA)
  • Manufacture And Refinement Of Metals (AREA)
  • Safety Valves (AREA)
  • Sampling And Sample Adjustment (AREA)
  • Heat Treatment Of Steel (AREA)
EP03405013A 2003-01-16 2003-01-16 Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit Withdrawn EP1441041A1 (de)

Priority Applications (18)

Application Number Priority Date Filing Date Title
EP03405013A EP1441041A1 (de) 2003-01-16 2003-01-16 Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit
EP03789376A EP1587965B1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit
DK03789376T DK1587965T3 (da) 2003-01-16 2003-12-20 Aluminiumslegering med höj styrke og lav bratkölingsfölsomhed
PL376309A PL203780B1 (pl) 2003-01-16 2003-12-20 Stop aluminium oraz sposób wytwarzania płyt z tego stopu i ich zastosowanie
US10/541,788 US20060096676A1 (en) 2003-01-16 2003-12-20 Aluminium alloy with increased resistance and low quench sensitivity
AU2003293963A AU2003293963A1 (en) 2003-01-16 2003-12-20 Aluminium alloy with increased resistance and low quench sensitivity
CA2513333A CA2513333C (en) 2003-01-16 2003-12-20 Aluminium alloy with increased resistance and low quench sensitivity
PT03789376T PT1587965E (pt) 2003-01-16 2003-12-20 ''liga de alumínio com elevada resistência e baixa sensibilidade à têmpera''
AT03789376T ATE367456T1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit
ES03789376T ES2290544T3 (es) 2003-01-16 2003-12-20 Aleacion de aluminio con una alta resistencia mecanica y una pequeña sensibilidad al enfriamiento brusco.
RU2005125727/02A RU2351674C2 (ru) 2003-01-16 2003-12-20 Толстостенная плита из алюминиевого сплава с высокой прочностью и малой чувствительностью к быстрому охлаждению (варианты) и способ ее изготовления (варианты)
PCT/EP2003/014696 WO2004063407A1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit
SI200330959T SI1587965T1 (sl) 2003-01-16 2003-12-20 Aluminijeva zlitina z visoko trdnostjo in majhno občutljivostjo za gašenje
DE50307736T DE50307736D1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit
TW092136857A TWI291993B (en) 2003-01-16 2003-12-25 Aluminium alloy exhibiting high mechanical strength and low quench sensitivity
HR20050704A HRP20050704B1 (en) 2003-01-16 2005-08-09 Aluminium alloy with increased resistance and low quench sensitivity
NO20053832A NO340750B1 (no) 2003-01-16 2005-08-15 Aluminiumlegering med høy fasthet og lav bråkjølingsfølsomhet, og anvendelser derav for fremstilling av plater.
US12/402,966 US7901522B2 (en) 2003-01-16 2009-03-12 Aluminum alloy with increased resistance and low quench sensitivity

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP03405013A EP1441041A1 (de) 2003-01-16 2003-01-16 Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit

Publications (1)

Publication Number Publication Date
EP1441041A1 true EP1441041A1 (de) 2004-07-28

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Family Applications (2)

Application Number Title Priority Date Filing Date
EP03405013A Withdrawn EP1441041A1 (de) 2003-01-16 2003-01-16 Aluminiumlegierung mit hoher Festigkeit und geringer Abschreckempfindlichkeit
EP03789376A Expired - Lifetime EP1587965B1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit

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EP03789376A Expired - Lifetime EP1587965B1 (de) 2003-01-16 2003-12-20 Aluminiumlegierung mit hoher festigkeit und geringer abschreckempfindlichkeit

Country Status (16)

Country Link
US (2) US20060096676A1 (sl)
EP (2) EP1441041A1 (sl)
AT (1) ATE367456T1 (sl)
AU (1) AU2003293963A1 (sl)
CA (1) CA2513333C (sl)
DE (1) DE50307736D1 (sl)
DK (1) DK1587965T3 (sl)
ES (1) ES2290544T3 (sl)
HR (1) HRP20050704B1 (sl)
NO (1) NO340750B1 (sl)
PL (1) PL203780B1 (sl)
PT (1) PT1587965E (sl)
RU (1) RU2351674C2 (sl)
SI (1) SI1587965T1 (sl)
TW (1) TWI291993B (sl)
WO (1) WO2004063407A1 (sl)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100363146C (zh) * 2005-05-20 2008-01-23 东北轻合金有限责任公司 浮桥用铝合金型材的制造方法
CN100523242C (zh) * 2006-11-13 2009-08-05 上海昊华模具有限公司 车用子午线轮胎模具用铝合金

Families Citing this family (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP1683882B2 (de) 2005-01-19 2010-07-21 Otto Fuchs KG Abschreckunempfindliche Aluminiumlegierung sowie Verfahren zum Herstellen eines Halbzeuges aus dieser Legierung
KR20080109938A (ko) 2006-05-18 2008-12-17 가부시키가이샤 고베 세이코쇼 알루미늄 합금 후판의 제조방법 및 알루미늄 합금 후판
EP2288738B1 (en) 2008-06-24 2014-02-12 Aleris Rolled Products Germany GmbH Al-zn-mg alloy product with reduced quench sensitivity
DE102008053893B4 (de) * 2008-10-30 2010-08-19 Audi Ag Vorrichtung und Verfahren zum Kühlen wenigstens eines Gussbauteils
RU2457422C2 (ru) * 2010-04-16 2012-07-27 Российская Федерация в лице Министерства промышленности торговли Российской Федерации Способ изготовления слоистой плиты на основе алюминия для противопульной сварной брони
FR2968675B1 (fr) 2010-12-14 2013-03-29 Alcan Rhenalu Produits epais en alliage 7xxx et procede de fabrication
RU2489217C1 (ru) * 2011-12-27 2013-08-10 Открытое акционерное общество "Всероссийский институт легких сплавов" (ОАО "ВИЛС") Способ производства листов из термически упрочняемых алюминиевых сплавов, легированных скандием и цирконием
JP6344923B2 (ja) * 2014-01-29 2018-06-20 株式会社Uacj 高強度アルミニウム合金及びその製造方法
CN109890663B (zh) 2016-08-26 2023-04-14 形状集团 用于横向弯曲挤压成形铝梁从而温热成型车辆结构件的温热成型工艺和设备
WO2018063024A1 (ru) * 2016-09-30 2018-04-05 Общество с ограниченной ответственностью "Объединенная Компания РУСАЛ Инженерно-технологический центр" Способ получения деформированных полуфабрикатов из сплавов на основе алюминия
MX2019004494A (es) 2016-10-24 2019-12-18 Shape Corp Metodo de formacion y procesamiento termico de aleacion de aluminio de multiples etapas para la produccion de componentes de vehiculo.
CN112921220A (zh) * 2021-01-25 2021-06-08 西南铝业（集团）有限责任公司 一种Al-Zn-Cu-Mg铸锭及其制备方法

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US3694272A (en) * 1970-12-24 1972-09-26 Kaiser Aluminium Chem Corp Method for forming aluminum sheet
FR2341661A1 (fr) * 1976-02-18 1977-09-16 Vmw Ranshofen Berndorf Ag Alliage de fonte d'aluminium soudable, plus faconnable a chaud, resistant mieux a la corrosion et ayant en meme temps de meilleures proprietes mecaniques
JPH0570910A (ja) * 1991-04-01 1993-03-23 Sumitomo Light Metal Ind Ltd 溶接構造用アルミニウム合金軟質材の製造方法
JPH07252573A (ja) * 1994-03-17 1995-10-03 Kobe Steel Ltd 靭性に優れたＡｌ−Ｚｎ−Ｍｇ−Ｃｕ系合金及びその製造方法
JPH10168553A (ja) * 1996-12-12 1998-06-23 Sumitomo Light Metal Ind Ltd 耐応力腐食割れ性に優れた高力アルミニウム合金押出管の製造方法

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US4618382A (en) * 1983-10-17 1986-10-21 Kabushiki Kaisha Kobe Seiko Sho Superplastic aluminium alloy sheets
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MX9204270A (es) * 1991-07-23 1993-01-01 Alcan Int Ltd Aleacion de aluminio mejorada.
US5961752A (en) * 1994-04-07 1999-10-05 Northwest Aluminum Company High strength Mg-Si type aluminum alloy
JP4204650B2 (ja) 1996-12-09 2009-01-07 三井金属鉱業株式会社 高強度耐熱亜鉛合金及び成形品
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FR2341661A1 (fr) * 1976-02-18 1977-09-16 Vmw Ranshofen Berndorf Ag Alliage de fonte d'aluminium soudable, plus faconnable a chaud, resistant mieux a la corrosion et ayant en meme temps de meilleures proprietes mecaniques
JPH0570910A (ja) * 1991-04-01 1993-03-23 Sumitomo Light Metal Ind Ltd 溶接構造用アルミニウム合金軟質材の製造方法
JPH07252573A (ja) * 1994-03-17 1995-10-03 Kobe Steel Ltd 靭性に優れたＡｌ−Ｚｎ−Ｍｇ−Ｃｕ系合金及びその製造方法
JPH10168553A (ja) * 1996-12-12 1998-06-23 Sumitomo Light Metal Ind Ltd 耐応力腐食割れ性に優れた高力アルミニウム合金押出管の製造方法

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Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100363146C (zh) * 2005-05-20 2008-01-23 东北轻合金有限责任公司 浮桥用铝合金型材的制造方法
CN100523242C (zh) * 2006-11-13 2009-08-05 上海昊华模具有限公司 车用子午线轮胎模具用铝合金

Also Published As

Publication number Publication date
TWI291993B (en) 2008-01-01
NO20053832D0 (no) 2005-08-15
ATE367456T1 (de) 2007-08-15
CA2513333A1 (en) 2004-07-29
EP1587965A1 (de) 2005-10-26
TW200427850A (en) 2004-12-16
SI1587965T1 (sl) 2007-12-31
NO340750B1 (no) 2017-06-12
US7901522B2 (en) 2011-03-08
NO20053832L (no) 2005-10-17
HRP20050704B1 (en) 2008-06-30
PL376309A1 (en) 2005-12-27
AU2003293963A1 (en) 2004-08-10
HRP20050704A2 (en) 2006-02-28
US20090223608A1 (en) 2009-09-10
PL203780B1 (pl) 2009-11-30
RU2005125727A (ru) 2007-02-27
ES2290544T3 (es) 2008-02-16
PT1587965E (pt) 2007-10-12
CA2513333C (en) 2010-09-14
WO2004063407A1 (de) 2004-07-29
DE50307736D1 (de) 2007-08-30
RU2351674C2 (ru) 2009-04-10
DK1587965T3 (da) 2007-11-19
US20060096676A1 (en) 2006-05-11
EP1587965B1 (de) 2007-07-18

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