US20060070686A1 - High hardness moulding plate and method for producing said plate - Google Patents

High hardness moulding plate and method for producing said plate Download PDF

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Publication number
US20060070686A1
US20060070686A1 US11/240,629 US24062905A US2006070686A1 US 20060070686 A1 US20060070686 A1 US 20060070686A1 US 24062905 A US24062905 A US 24062905A US 2006070686 A1 US2006070686 A1 US 2006070686A1
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United States
Prior art keywords
moulding plate
plate according
range
hardness
moulding
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Abandoned
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US11/240,629
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English (en)
Inventor
Claus Jurgen Moritz
Jorgen Van De Langkruis
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Novelis Koblenz GmbH
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Corus Aluminium Walzprodukte GmbH
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Assigned to CORUS ALUMINIUM WALZPRODUKTE GMBH reassignment CORUS ALUMINIUM WALZPRODUKTE GMBH ASSIGNMENT OF ASSIGNORS INTEREST (SEE DOCUMENT FOR DETAILS). Assignors: MORITZ, CLAUS JURGEN, VAN DE LANGKRUIS, JORGEN
Publication of US20060070686A1 publication Critical patent/US20060070686A1/en
Abandoned 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
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent

Definitions

  • the invention relates to moulding plate of an aluminium wrought alloy.
  • the invention further relates to a method for producing said moulding plate.
  • tooling and moulding plate market for blow moulding and thermoforming of rubbers and plastic, a sustained effort in reducing costs is made whilst maintaining satisfactory wear resistance and repair weldability.
  • tooling plates are also widely used in many other industrial applications, including components produced by various machining operations such as drilling, milling and turning.
  • Commonly used tooling plates are made from selected alloys from the AA2000 series alloys, the AA6000 series alloys or the AA7000-series alloys.
  • High wear resistance in combination with good machinability are important properties of alloys for moulding plate.
  • this wear resistance is obtained by alloying with copper (such as in the AA2000 series) or Zinc (such as in the AA7000 series) or magnesium and silicon (such as in the AA6000 series) in combination with a thermo-mechanical treatment.
  • copper such as in the AA2000 series
  • Zinc such as in the AA7000 series
  • magnesium and silicon such as in the AA6000 series
  • the typical way to achieve high hardness is via precipitation hardening of coherent phases. Additional hardening by relatively coarse particles, such as primary Si and incoherent Mg 2 Si is often considered inappropriate, because of the related risks of eutectic melting at elevated temperatures.
  • AA2000 and AA7000 alloys typically, higher hardness is achieved than with AA6000 alloys.
  • a disadvantage of the AA2000 series is the high copper content which makes the alloy expensive as well as very sensitive to the heat treatment.
  • the weldability of the alloy is adversely affected by the high copper content.
  • Similar arguments are made for the AA7000 series such as high residual stresses, and poor weldability and corrosion performance which cause complications with dimensional tolerances, repair weldability, and durability of the mould.
  • the wear resistance of an AA6000 series alloy in a T6 temper, such as AA6010, AA6013, AA6061, AA6066, AA6070 and AA6082 is usually adequate for normal industrial applications. However, for high performance applications a higher wear resistance is desired, without adversely affecting weldability and costs.
  • the present invention provides a moulding plate of an aluminium wrought alloy comprising, in weight percent: Si 1.4-2.1, Mn 0.8-1.2, Cu 0.45-0.9, Mg 0.7-1.2, Ti ⁇ 0.15, Zn ⁇ 0.4, Fe ⁇ 0.7, one or more of Zr, Cr, V each ⁇ 0.25, incidental elements and impurities, each ⁇ 0.05, total ⁇ 0.25, the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105 HB.
  • a method is provided of manufacturing a moulding plate.
  • FIG. 1 which is the sole figure, shows the hardness profiles of plates with a composition according to Example 7 with thicknesses of 80, 100 or 150 mm.
  • a moulding plate of an aluminium wrought alloy comprising, in weight percent:
  • T6 temper condition having a hardness of more than 105 HB.
  • the increased hardness is reached by combining precipitation hardening of Mg—Si—Cu phases, Fe- and Mn-containing intermetallics and dispersoids, which are known to actually reduce the age hardening effect in balanced AlMgSi(Cu) alloys through their effect on the quench sensitivity, with a high excess of Si, which decreases the Mg solute level, to minimise the negative effect of Mn-containing dispersoids on the quench sensitivity.
  • the supersaturation level for Mg—Si phases is not yet so high that particularly high quench sensitivities already result from the Mg-, Si-, and Cu solute content.
  • the balanced alloy composition according to the invention is believed to combine the strength increasing effect of a silicon addition with moderate amount of copper, magnesium and manganese.
  • this alloy provides satisfactory weldability and a hardness of at least 105 HB. It should be noted that the hardness values are expressed in the Brinell scale and were measured by a ball having a 2.5 mm diameter loaded with a mass of 62.5 kg. The hardness tests were performed according to ASTM E10 (version 2002).
  • the hardness in T6 temper condition is at least 115 HB, more preferably at least 120 HB. These hardness values imply an increased machinability as well as wear resistance.
  • the chemical composition in combination with a heat treatment ensures that adequate weldability and thus reparability is maintained: surprisingly it has been found that for Cu levels of up to 0.9% the plate alloy shows very good reparability with for instance a common 4043 filler wire.
  • the Si is in the range of 1.53-2.0%, more preferably in the range of 1.55-1.9%. It was found that this range of silicon provides a very good combination of the desirable properties, through hardening by coherent Mg—Si—Cu phases, and by primary Si, incoherent Mg 2 Si and ⁇ -Al(Fe,Mn,Cu)Si intermetallic phases and dispersoids.
  • the Mn is in the range of 0.85-1.10%. It was found that this range of manganese provides a very good combination of the desirable properties, in particular by stimulating the formation of ⁇ -Al(Fe,Mn,Cu)Si intermetallic phases and dispersoids. At high Si levels, the tendency to form the relatively brittle ⁇ -AlFeSi intermetallic phase increases. However, by ensuring the presence of suitable amounts of Mn and Cu the more favourable ⁇ -Al(Fe,Mn,Cu)Si phase is stabilised.
  • the Cu is in the range of 0.5-0.7%. It was found that this range of copper provides a very good combination of the desirable properties through coherent Mg—Si—Cu phases and stabilised ⁇ -Al(Fe,Mn,Cu)Si, whilst keeping alloying cost down and ensuring good repair weldability.
  • the Zn is below 0.3%, preferably in the range of 0.17-0.3%.
  • the Fe is preferably at least 0.2%, more preferably in the range 0.2-0.5%, and even more preferably in the range 0.3-0.5% to ensure the formation of sufficient amounts of hardness increasing ⁇ -Al(Fe,Mn,Cu)Si intermetallics.
  • the Zr, Cr, V are each preferably below 0.18%, more preferably below 0.12% to further reduce the quench sensitivity.
  • the moulding plate has a machinability rating of “B” or better as defined in ‘ASM Specialty Handbook—Aluminium and Aluminium Alloys (ed. J. R. Davis), ASM International 1993, pages 328-331.
  • the moulding plate has a final thickness of 300 mm, in which the claimed hardness values can still be met in the plate centre.
  • the final thickness is in the range of between 5 to 300 mm, more preferably in the range of between 5 to 260 mm. These thickness ranges allow the application of the moulding plate for all practical application involving moulding plate.
  • the moulding plate has been rolled to the final thickness by hot rolling only.
  • a method is provided of manufacturing a moulding plate comprising the subsequent (in other words “sequential”) steps of:
  • a moulding plate according to the invention By manufacturing a moulding plate according to the invention a high hardness product with a high content of chip-breaking intermetallics is obtained.
  • the cooling rate during the rapid cooling after solution heat treating is important because this cooling rate determines the amount of solute content of Mg, Si and Cu which were dissolved during the solution heat treatment.
  • the heat treatment after hot rolling or hot pressing is a T6-treatment.
  • the homogenisation temperature is at least 450° C., preferably at least 500° C., more preferably between 500 and 595° C., preferably for between 1 to 25 hours, more preferably for between 10 to 16 hours.
  • the pre-heat temperature is at least 570° C., between about 300° C. and 570° C., preferably between 350 and 530° C., preferably for between 1 to 25 hours, more preferably for between 1 and 10 hours.
  • the solution heat-treating temperature is at least 500° C., preferably at least 520° C. and more preferably at least 540° C.
  • the cooling rate after solution heat-treating from the solution heat-treating temperature to below 250° C., preferably to below 150° C. and more preferably to below 100° C. is at least 1° C./s, preferably at least 2° C./s more preferably 5° C./s, even more preferably at least 10° C./s. It should be noted that the cooling rate of the product during quenching is dependent on the location within the product. The centre of the product cools down more slowly than the surface of the product.
  • the critical point in the product is defined as the point where the cooling rate during quenching is the lowest.
  • the abovementioned cooling rates relate to the cooling rate at the critical point.
  • the ageing process comprises natural ageing for a maximum duration of 28 days, preferably for a maximum duration of 14 days, more preferably for a maximum duration of 7 days, even more preferably for a maximum duration of 2 days, followed by an artificial ageing treatment equivalent to ageing at about 180 to 200° C. for about 1-10 hours.
  • time and temperature of an annealing are usually not chosen independently.
  • the ageing process is thermally activated, resulting in the situation that a high temperature coupled with a short time is equivalent to a lower temperature and a longer time, i.e. the same metallurgical state is reached after the ageing treatment.
  • the working step comprises a rolling or pressing step.
  • the rolling step comprises a hot rolling and/or a hot pressing step and/or cold-rolling step.
  • the working step comprises hot rolling and/or hot pressing only.
  • the casting step is a near-net shape casting step, wherein the dimensions of the cast product approximates the final product.
  • alloys were homogenised at a temperature above 510° C., optionally hot rolled, solution heat treated at 550° C., cooled down with at least 10° C./s to maximise the solute content of Mg, Si and Cu, stored for 14 days at room temperature, and aged following an ageing treatment equivalent to 190° C. for 2-6 hours. In this way, a high-hardness T6-temper product with a high content of chip-breaking intermetallics is obtained, leading to a hardness of at least 120 HB.
  • Example 7 was solution heat treated at 530° C. and stored at room temperature for a period of 1 day, the remainder of the process conditions being as given above for the other alloys.
  • the hardness profiles of plates with the composition according to Example 7 with thicknesses of 80, 100 or 150 mm are shown in FIG. 1 .
  • the distance (L) to the centre of the plate in the thickness direction in mm is given, and along the Y-axis the hardness in HB values is given at different locations over the thickness of the plate. All measured values show a hardness value of at least 120 HB at every location over the thickness of the plate.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Conductive Materials (AREA)
  • Moulds For Moulding Plastics Or The Like (AREA)
  • Metal Rolling (AREA)
  • Heat Treatment Of Articles (AREA)
  • Chemical Treatment Of Metals (AREA)
  • Heat Treatment Of Steel (AREA)
  • Forging (AREA)
  • Laminated Bodies (AREA)
  • Polymerisation Methods In General (AREA)
US11/240,629 2004-10-05 2005-10-03 High hardness moulding plate and method for producing said plate Abandoned US20060070686A1 (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
EP04077718 2004-10-05
EP04077781.7 2004-10-05

Publications (1)

Publication Number Publication Date
US20060070686A1 true US20060070686A1 (en) 2006-04-06

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US11/240,629 Abandoned US20060070686A1 (en) 2004-10-05 2005-10-03 High hardness moulding plate and method for producing said plate

Country Status (9)

Country Link
US (1) US20060070686A1 (fr)
EP (1) EP1802782B1 (fr)
CN (1) CN100562595C (fr)
AT (1) ATE389736T1 (fr)
CA (1) CA2582249A1 (fr)
DE (2) DE102005047406A1 (fr)
ES (1) ES2302247T3 (fr)
FR (1) FR2876117B1 (fr)
WO (1) WO2006037647A1 (fr)

Cited By (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120156089A1 (en) * 2010-03-15 2012-06-21 Nissan Motor Co., Ltd. Aluminum alloy and high strength bolt made of aluminum alloy
CN108474065A (zh) * 2016-01-08 2018-08-31 奥科宁克公司 新型6xxx铝合金及其制备方法

Families Citing this family (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
DE102006039684B4 (de) * 2006-08-24 2008-08-07 Audi Ag Aluminium-Sicherheitsbauteil
WO2010081889A1 (fr) * 2009-01-16 2010-07-22 Aleris Aluminum Koblenz Gmbh Procédé de fabrication d'un produit de type tôle d'alliage d'aluminium présentant de faibles taux de contrainte résiduelle
US9314826B2 (en) 2009-01-16 2016-04-19 Aleris Rolled Products Germany Gmbh Method for the manufacture of an aluminium alloy plate product having low levels of residual stress
CN102548751B (zh) * 2009-10-08 2015-03-25 阿莱利斯铝业迪弗尔私人有限公司 具有铝合金芯管的多层管
SI24911A (sl) 2016-03-04 2016-07-29 Impol 2000, d.d. Visokotrdna aluminijeva zlitina Al-Mg-Si in njen postopek izdelave
CN107245614B (zh) * 2017-07-27 2019-01-22 广州致远新材料科技有限公司 一种耐磨铝合金及其用途
CN108300907B (zh) * 2018-02-10 2020-07-21 沈阳航空航天大学 一种Al-Mn-Si-Mg合金材料及其制备方法
CN109136670B (zh) * 2018-08-21 2019-11-26 中南大学 一种6xxx系铝合金及其制备方法
CN112430766B (zh) * 2020-11-03 2022-02-18 福建祥鑫股份有限公司 一种高强低屈强比6系铝合金及其制备方法
JP2022150384A (ja) * 2021-03-26 2022-10-07 本田技研工業株式会社 アルミニウム合金、積層造形物の製造方法および積層造形物
CN114277268B (zh) * 2021-12-24 2023-04-07 东北轻合金有限责任公司 一种用于钎焊的铝合金箔材的制造方法

Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5690758A (en) * 1993-12-28 1997-11-25 Kaiser Aluminum & Chemical Corporation Process for the fabrication of aluminum alloy sheet having high formability
US6004409A (en) * 1997-01-24 1999-12-21 Kaiser Aluminum & Chemical Corporation Production of high quality machinable tolling plate using brazing sheet scrap

Family Cites Families (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH04325650A (ja) * 1991-04-24 1992-11-16 Kobe Steel Ltd 金型用アルミニウム合金とその製造方法
JPH04325645A (ja) * 1991-04-25 1992-11-16 Furukawa Alum Co Ltd 焼付け硬化後の強度に優れたアルミニウム合金およびその製造方法
JP2823797B2 (ja) * 1994-02-16 1998-11-11 住友軽金属工業株式会社 成形加工用アルミニウム合金板の製造方法
US5961752A (en) * 1994-04-07 1999-10-05 Northwest Aluminum Company High strength Mg-Si type aluminum alloy
FR2726007B1 (fr) * 1994-10-25 1996-12-13 Pechiney Rhenalu Procede de fabrication de produits en alliage alsimgcu a resistance amelioree a la corrosion intercristalline
JP3324093B2 (ja) * 1999-08-25 2002-09-17 古河電気工業株式会社 自動車部材向け鍛造加工用アルミニウム合金材及び鍛造加工自動車部材
FR2807449B1 (fr) * 2000-04-07 2002-10-18 Pechiney Rhenalu Procede de fabrication d'elements de structure d'avions en alliage d'aluminium al-si-mg
EP1167560B1 (fr) * 2000-06-27 2010-04-14 Corus Aluminium Voerde GmbH Alliage de coulée à base d'aluminium

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US5690758A (en) * 1993-12-28 1997-11-25 Kaiser Aluminum & Chemical Corporation Process for the fabrication of aluminum alloy sheet having high formability
US6004409A (en) * 1997-01-24 1999-12-21 Kaiser Aluminum & Chemical Corporation Production of high quality machinable tolling plate using brazing sheet scrap

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20120156089A1 (en) * 2010-03-15 2012-06-21 Nissan Motor Co., Ltd. Aluminum alloy and high strength bolt made of aluminum alloy
US8852364B2 (en) * 2010-03-15 2014-10-07 Nissan Motor Co., Ltd. Aluminum alloy and high strength bolt made of aluminum alloy
CN108474065A (zh) * 2016-01-08 2018-08-31 奥科宁克公司 新型6xxx铝合金及其制备方法

Also Published As

Publication number Publication date
EP1802782B1 (fr) 2008-03-19
ATE389736T1 (de) 2008-04-15
WO2006037647A1 (fr) 2006-04-13
DE602005005509D1 (de) 2008-04-30
CN101035919A (zh) 2007-09-12
FR2876117B1 (fr) 2007-10-26
FR2876117A1 (fr) 2006-04-07
DE102005047406A1 (de) 2006-06-01
DE602005005509T2 (de) 2009-04-16
CN100562595C (zh) 2009-11-25
ES2302247T3 (es) 2008-07-01
EP1802782A1 (fr) 2007-07-04
CA2582249A1 (fr) 2006-04-13

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