EP4186988A1 - Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée - Google Patents

Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée Download PDF

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Publication number
EP4186988A1
EP4186988A1 EP21210907.8A EP21210907A EP4186988A1 EP 4186988 A1 EP4186988 A1 EP 4186988A1 EP 21210907 A EP21210907 A EP 21210907A EP 4186988 A1 EP4186988 A1 EP 4186988A1
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EP
European Patent Office
Prior art keywords
holding
range
casting
temperature
cast part
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.)
Pending
Application number
EP21210907.8A
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German (de)
English (en)
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EP4186988A9 (fr
Inventor
Werner FRAGNER
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.)
AMAG casting GmbH
Original Assignee
AMAG casting 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 AMAG casting GmbH filed Critical AMAG casting GmbH
Priority to EP21210907.8A priority Critical patent/EP4186988A1/fr
Publication of EP4186988A1 publication Critical patent/EP4186988A1/fr
Publication of EP4186988A9 publication Critical patent/EP4186988A9/fr
Pending 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
    • 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
    • C22F1/043—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 silicon as the next major constituent

Definitions

  • the invention has therefore set itself the task of improving a method of the type described at the outset in such a way that a cast part with precise shape can be produced reproducibly with almost comparatively high elongation at break and tensile strength values.
  • the invention solves the problem set by the features of claim 1.
  • the heat treatment includes a second hold at a second hold temperature in the range of 150 to 250 °C during a second hold time and a subsequent, second, accelerated cooling
  • a second hold at a second hold temperature in the range of 150 to 250 °C during a second hold time and a subsequent, second, accelerated cooling
  • the latter can be specifically avoided by the provision for interrupting the first hold, since the second hold with subsequent second accelerated cooling interrupts the first hold several times and this first holding is thereby divided into holding sections, each at a first holding temperature in the range from 60 to 140° C. and during a first holding time section which lasts longer than the second holding time.
  • the remainder of the cast aluminum alloy is aluminum and impurities that are unavoidable due to production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • accelerated cooling can be understood to mean faster cooling than cooling at room temperature and still air, e.g. quenching (cf. Friedrich Ostermann, Aluminum Application Technology, 3rd edition, year of publication 2014 : Cooling after solution annealing and Aluminum Paperback, Part 2, 16th edition, S476, Aluminum-Verlag (2009 ) or Campbell J.: Castings Practices, The 10 Rules of Castings, Oxford, S168-S174, Elsevier Butterworth-Heinemann Verlag (2004 )).
  • quenching cf. Friedrich Ostermann, Aluminum Application Technology, 3rd edition, year of publication 2014 : Cooling after solution annealing and Aluminum Paperback, Part 2, 16th edition, S476, Aluminum-Verlag (2009 ) or Campbell J.: Castings Practices, The 10 Rules of Castings, Oxford, S168-S174, Elsevier Butterworth-Heinemann Verlag (2004 )).
  • the first holding temperature is preferably in the range from 80 to 130° C. in order to still be able to ensure a comparatively high Mg-Si cluster formation in the aluminum casting alloy with shorter first holding time sections.
  • the above can be further improved by a first holding temperature in the range from 100 to 120 °C.
  • the first holding periods are preferably less than or equal to 10 hours in order to use essentially all scarred vacancies for the formation of Mg-Si clusters.
  • the first holding time intervals are in the range from 1 to 6 Hours to use a sufficient number of scared vacancies to form Mg-Si clusters.
  • the above can be further improved by first holding periods in the range of 2 to 4 hours.
  • the second holding temperature is in the range from 170 to 250 °C
  • a temperature range can be specified in which, taking into account a comparatively short second holding time, with a reduced tendency to ⁇ " precipitations, a large number of vacancies can advantageously be generated.
  • the above is due to a second Holding temperature in the range from 200 to 240 °C can be further improved.
  • the second holding time of the second holding is preferably less than or equal to 15 minutes in order to create sufficient voids with a low tendency to precipitate in the cast alloy.
  • the second hold time of the second hold is preferably less than or equal to 10 minutes, in particular it is in the range from 5 seconds to 5 minutes.
  • this average crystal grain size can be measured at any time after the first accelerated cooling.
  • the average crystal grain size (KG) can be done after the first accelerated cooling and before the first or second holding.
  • the first soak temperatures are the same throughout the first soak.
  • several or all of the first holding periods are the same.
  • the repeated second holding at a second holding temperature is the same for a second holding time.
  • the first holding time section of the first holding time sections preferably lasts longer than the subsequent first holding time sections.
  • the first and/or second accelerated cooling takes place at a cooling rate of at least 20° C./s, in particular at least 50° C./s, preferably at least 80° C./s, in order to reliably remove the voids formed during the second hold to be able to scare.
  • the heating from the first holding to the second holding preferably takes place at a heating rate of at least 10° C./s, in particular at least 50° C./s.
  • the aluminum alloy is preferably of type EN AC-42100 (or AlSi7Mg0.3 according to DIN EN 1706:2020), EN AC-42200 (or AlSi7Mg0.6 according to DIN EN 1706:2020) or EN AC-43500 (AlSi10MgMn according to DIN EN1706:2020).
  • the cast part preferably has a wall thickness of 1 to 10 mm (millimeters), in particular 2 to 6 mm, at least in sections, in order to create a sufficient number of voids and to prevent unwanted precipitation when the first hold is briefly interrupted.
  • the solution annealing of the cast part preferably takes place at an annealing temperature in the range from 400 to 500° C. in order to further reduce the risk of residual stresses. All the more so when the casting is solution annealed at an annealing temperature in the range of 420 to 480 °C.
  • the casting is preferably solution annealed with an annealing hold time in the range from 30 minutes to 4 hours.
  • the casting can be solution annealed with an annealing hold time in the range of 1.5 to 2.5 hours.
  • the invention has set itself the task of creating a dimensionally accurate cast part, for example a pressure die-cast part, which is subjected to hardening and has comparatively high elongation at break and tensile strength values.
  • the invention solves the problem set by the features of claim 13.
  • the aluminum alloy preferably has a cluster density of at least 2 ⁇ 10 24 clusters/m 3 with a Guinier radius >1 nm (nanometers) and with a median Guinier radius of >1.3 nm, measured using atom probe tomography (LEAP). Type LEAP 3000HR, on.
  • the width of the precipitation-free zones at the grain boundaries is between 5 and 100 nm (nanometers) (measured using a scanning transmission electron microscope (HAADF images at 17,000x magnification, Talos F200X G2 S-TEM)) to avoid a negative impact on the strain values of the to limit the casting - all the more so when the width of the precipitation-free zones at the grain boundaries is between 20 and 80 nm.
  • the precipitations containing Mg and Si, in particular of the Mg 2 Si type preferably have an average size of 30 to 100 nm (nanometers) at the grain boundaries (measured using a scanning transmission electron microscope (HAADF images at 17,000x magnification, Talos F200X G2 S -TEM)) in order to be able to ensure sufficient strength at high strain values - especially when the precipitations at the grain boundaries have an average size of 50 to 70 nm.
  • FIG. 1 shows a view of the sequence of the method according to the invention for hardening a cast part made of an aluminum cast alloy.
  • Castings namely die-castings, A and B each with a wall thickness of 3 mm (millimeters) and an AlSi10MgMn according to DIN EN 1706:2020 cast aluminum alloy were used to demonstrate the effects achieved Si wt% mg wt% Mn wt% Fe wt% Cu wt% Zn wt% Ti wt% Srppm 10.1 0.35 0.52 0.09 0.03 0.07 0.12 180 and the remainder being aluminum and impurities unavoidable due to production, each with a maximum of 0.05% by weight and a maximum of 0.15% by weight in total.
  • This method is known from the prior art, in which the casting A is subjected to solution annealing at 510° C. (degrees Celsius) for 6 h (hours) and a subsequent first accelerated cooling (namely water quenching). This is followed by a single-stage heat treatment consisting of a first holding with a first holding temperature (T1) at 170° C. and a first holding time (h1) of 8 h (hours).
  • T1 first holding temperature
  • h1 first holding time
  • process V2 In contrast to process V1, among other things, the heat treatment of process V2 according to the invention is multi-stage - as in 1 can be seen.
  • This multi-stage structure is formed by interrupting a first holding four times by a second holding together with a second, accelerated cooling. As a result, the first hold is divided into hold sections.
  • first holding time sections h1a or h1b, h1c, h1d, h1e differ from one another on the one hand in the first holding time sections h1a or h1b, h1c, h1d, h1e, and on the other hand are the same in the first holding temperature T1--although the latter does not necessarily have to be the case.
  • Each holding section can have its individual holding temperature T1 during the individual first holding time section h1a, h1b, h1c, h1d or h1e.
  • the first holding temperature T1 or first holding temperatures T1 of the first holding time sections h1a, h1b, h1c, h1d, h1e only have to meet the condition of 60 to 140°C.
  • the first holding time sections h1a, h1b, h1c, h1d and h1e last significantly longer than the second holding time h2 (cf. hours in relation to seconds).
  • casting B achieves improved mechanical properties - as is the case with casting A.
  • cast part B has a significantly higher dimensional accuracy compared to cast part A than is the case with cast part A, for which a higher dimensional deviation was found.
  • a dimensionally accurate cast part can therefore be created using method V2, with which outstanding elongation at break and tensile strength values can also be achieved due to the hardening of the aluminum alloy with the formation of essentially Mg-Si clusters.

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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)
EP21210907.8A 2021-11-26 2021-11-26 Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée Pending EP4186988A1 (fr)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP21210907.8A EP4186988A1 (fr) 2021-11-26 2021-11-26 Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
EP21210907.8A EP4186988A1 (fr) 2021-11-26 2021-11-26 Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée

Publications (2)

Publication Number Publication Date
EP4186988A1 true EP4186988A1 (fr) 2023-05-31
EP4186988A9 EP4186988A9 (fr) 2023-12-27

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EP21210907.8A Pending EP4186988A1 (fr) 2021-11-26 2021-11-26 Procédé de durcissement d'une pièce de coulée en alliage d'aluminium et pièce de coulée ainsi fabriquée

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Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3825428A1 (fr) * 2019-11-25 2021-05-26 AMAG casting GmbH Composant moulé sous pression et procédé de fabrication d'un composant moulé sous pression

Patent Citations (1)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3825428A1 (fr) * 2019-11-25 2021-05-26 AMAG casting GmbH Composant moulé sous pression et procédé de fabrication d'un composant moulé sous pression

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