EP3250722A1 - Process for obtaining a low silicon aluminium alloy part - Google Patents
Process for obtaining a low silicon aluminium alloy partInfo
- Publication number
- EP3250722A1 EP3250722A1 EP16703341.4A EP16703341A EP3250722A1 EP 3250722 A1 EP3250722 A1 EP 3250722A1 EP 16703341 A EP16703341 A EP 16703341A EP 3250722 A1 EP3250722 A1 EP 3250722A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- shells
- level
- precipitates
- preform
- 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
Links
- 238000000034 method Methods 0.000 title claims abstract description 20
- 239000010703 silicon Substances 0.000 title claims abstract description 15
- 229910052710 silicon Inorganic materials 0.000 title claims abstract description 15
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 7
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 title abstract description 14
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 29
- 239000000956 alloy Substances 0.000 claims abstract description 29
- 239000010949 copper Substances 0.000 claims abstract description 16
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 238000005266 casting Methods 0.000 claims abstract description 7
- 229910052712 strontium Inorganic materials 0.000 claims abstract description 5
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 claims abstract description 5
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims abstract description 4
- 239000011777 magnesium Substances 0.000 claims abstract description 4
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 4
- 239000010936 titanium Substances 0.000 claims abstract description 4
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 4
- 238000003825 pressing Methods 0.000 claims abstract description 3
- 238000010438 heat treatment Methods 0.000 claims description 9
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 239000011572 manganese Substances 0.000 claims description 6
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 5
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 claims description 4
- 230000002301 combined effect Effects 0.000 claims description 2
- 238000004381 surface treatment Methods 0.000 claims description 2
- 230000000694 effects Effects 0.000 abstract description 6
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 abstract description 3
- 238000004898 kneading Methods 0.000 abstract 1
- 238000003303 reheating Methods 0.000 abstract 1
- 239000002244 precipitate Substances 0.000 description 19
- 238000007711 solidification Methods 0.000 description 15
- 230000008023 solidification Effects 0.000 description 15
- 238000005242 forging Methods 0.000 description 9
- 230000007547 defect Effects 0.000 description 8
- 230000005496 eutectics Effects 0.000 description 6
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 5
- 239000000203 mixture Substances 0.000 description 5
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 230000035945 sensitivity Effects 0.000 description 4
- 238000004090 dissolution Methods 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 239000011265 semifinished product Substances 0.000 description 3
- 229910000676 Si alloy Inorganic materials 0.000 description 2
- 238000001816 cooling Methods 0.000 description 2
- 229910052742 iron Inorganic materials 0.000 description 2
- 238000004519 manufacturing process Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- AZDRQVAHHNSJOQ-UHFFFAOYSA-N alumane Chemical group [AlH3] AZDRQVAHHNSJOQ-UHFFFAOYSA-N 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000015556 catabolic process Effects 0.000 description 1
- 230000006378 damage Effects 0.000 description 1
- 238000006731 degradation reaction Methods 0.000 description 1
- 230000008030 elimination Effects 0.000 description 1
- 238000003379 elimination reaction Methods 0.000 description 1
- 238000001125 extrusion Methods 0.000 description 1
- 229910001338 liquidmetal Inorganic materials 0.000 description 1
- 150000002696 manganese Chemical class 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 235000011837 pasties Nutrition 0.000 description 1
- 230000007226 seed germination Effects 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D27/00—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting
- B22D27/09—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting by using pressure
- B22D27/11—Treating the metal in the mould while it is molten or ductile ; Pressure or vacuum casting by using pressure making use of mechanical pressing devices
-
- 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
-
- 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
- C22C21/04—Modified aluminium-silicon alloys
-
- 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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
-
- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Definitions
- the invention relates to the technical sector of the foundry, for the manufacture of aluminum parts, particularly in the field of automotive, aerospace and more generally, all types of industries.
- the alloys mentioned have been developed for obtaining semi-finished products (billets or ingots for forging or rolling) intended to be transformed during hot or cold operations with high deformation rates (> 50%).
- the geometries of these semi-finished products are simple (bar, bar or ingot) which makes it possible to solidify these alloys with a minimum of defects by using processes with high solidification rates.
- These geometries and these processes lead, according to currently controlled techniques, to semi-finished products free from defects among which we can mention: shrinkage, cracks, macro-segregations, macro-precipitation (prevents the formation of too coarse precipitates,> 100 ⁇ ).
- the problem posed that the invention proposes to solve is to be able to produce parts responding to standards of quality and safety, and likely to have complex shapes.
- the object of the invention relates to a method of manufacturing a piece of low silicon aluminum alloy, type 6000.
- the invention relates to a process for obtaining a low silicon aluminum alloy part, comprising silicon at a level of between 0.5 and 3%, magnesium at a rate of between 0.65 and 1%, copper at a level between 0.20 and 0.40%, manganese at a rate of between 0.15 and 0.25%, titanium at a level between 0.10 and 0.20% , and strontium at a level between 0 and 120 ppm, according to which:
- said alloy is cast in a mold to obtain the part
- said preform is cooled and then subjected to an operation capable of heating it to a temperature of between 470.degree. C. and 550.degree.
- said part is positioned between two shells of a matrix defining a footprint of substantially equal dimensions, but smaller than that of the mold,
- the two shells are strongly pressed against each other to exert on the piece disposed between said shells a combined effect of pressing and surface treatment.
- the present invention also objects:
- the latter is heated by being placed in a tunnel oven. It follows from these characteristics that the foundry operation followed by the one-step forging of the preform do not have the same temperature parameters, solidification rate, deformation rate, forging temperature as the processes of the prior state of the preform. the technique.
- the geometry of the preform unlike bars or ingots, comprises from its conception the blanks of the functional areas of the part and can therefore have a complex geometry comprising ribs or sectional variations leading to isolated masses of liquid metal.
- These insulated masses can be "tolerated” by increasing the silicon content (AS7G03 type, standard foundry alloy). A decrease in this rate makes the alloy more sensitive during solidification and leads to more numerous and larger volume shrinkage defects (porosities).
- the solidification range which is defined by the difference between the liquidus temperature and the eutectic temperature of the alloy considered. For an alloy, type AS7G03 modified with strontium, this interval is 50 ° C approx. (61 1 ° C - 562 ° C).
- TAS7G03 has almost no sensitivity to crack because of the large amount of eutectic that will be able to fill the cracks that appear during solidification shrinkage. This is not the case of a low silicon alloy, which has very little eutectic which causes a high sensitivity to the crack and requires to adapt the composition and to control the thermal gradients of solidification. It is also necessary to adjust the chemical composition to obtain the best compromise between the foundry, forging, heat treatment parameters and the desired mechanical characteristics on finished parts. For this purpose we detail below each of the elements of the alloy, their content and the effects that led to retain these values:
- the silicon content is between 0.5 and 3%.
- a silicon content of less than 1% leads to the highest elastic limits and elongations. However, this is the rate at which the alloy is most sensitive to crack and has the lowest flowability. It is therefore necessary to be able to adapt the silicon content according to the geometry of the part. Complex geometries will require a higher rate to reduce this crack sensitivity.
- the maximum rate of 3% corresponds to a rate beyond which the elongation and the elastic limit become too low so that it is always interesting to produce with an alloy of this type.
- the magnesium level is between 0, 65 and 1%. This rate makes it possible to optimize the density of Mg 2 Si precipitates in the aluminum matrix. It compensates for the decrease in silicon content while having a minimum of macroscopic Mg 2 Si precipitates that are damaging and must be dissolved or transformed during heat treatment. If the precipitates are too numerous, or too big, the heat treatment will have a weak effect for their dissolution, the critical size of dissolution having been exceeded.
- the copper content is between 0.20 and 0.40%. This rate allows the formation of Al 2 Cu precipitates in the matrix and the total absence of macroscopic Al 2 Cu precipitates. The absence of these macroscopic precipitates makes it possible to maintain high forging temperatures and thus to minimize forging efforts (which is carried out in a single step). Indeed, the main precipitates formed in the presence of copper are Al 2 Cu and AlMgSiCu respectively melting at 490 ° C and 525 ° C, their presence would prevent forging at higher temperatures without risk of burning of the alloy that would make the parts unusable. This degradation is similar to a destruction of the alloy.
- a higher copper content also increases the crack sensitivity of the alloy, because there remains a eutectic to be solidified at low temperatures (490 ° C or 525 ° C) for which the mechanical stresses (related to the removal of solidification) exercised on the piece are important.
- the manganese content is between 0.15 and 0.25%. This rate avoids the formation of AlFeSi precipitates in ⁇ -form (very damaging plate) and makes it possible to form AlFeMnSi precipitates in a form (less damaging Chinese writing). This maximizes the finished part elongation resulting from the Cobapress process. This effect is most often used with larger amounts of manganese and iron, these two elements leading to a hardening of the alloy but also to larger precipitates during solidification.
- the alloy according to the invention is intended, as indicated, the Cobapress process, which is forged in a single step, which does not have the large deformations encountered in forging, rolling or extrusion. These large deformations can break these large precipitates and make them much less damaging while maintaining their hardening effect.
- the impact of the iron-based precipitates on the mechanical characteristics should be minimized as soon as they are poured. Indeed, their morphology will not be changed, the forge in one step does not deform the room enough to change their morphology.
- this manganese content is adapted to the cooling rates obtained during casting in a permanent mold, with respect to these speeds, it promotes the formation of AlFeMnSi precipitates in the form a.
- the titanium content is between 0.10 and 0.20%. This rate is necessary for efficient seed germination and fine grain size which has a significant effect on the mechanical characteristics of these alloys.
- the strontium level is between 0 and 120 ppm. This rate is necessary to have a fibrous solidification of the small amounts of eutectic that are formed. This occurs mainly for silicon levels higher than 1.5%.
- composition of this alloy is adapted to lead to a solidification which will maximize the mechanical characteristics despite the low levels of deformation encountered during the Cobapress process.
- the forging operation Cobapress allows to close and rewrite these defects with a control in design of the rate of deformation.
- the temperature / deformation couple allows a rectification of the defects.
- the table below shows the mechanical properties on casting and parts, according to the Cobapress process, after T6 heat treatment of the low silicon alloy. We can note the improvement of rupture limit Rm and elongation at break:
- this composition makes it possible to reduce the complexity of the usual heat treatment for Al-Mg-Si-Cu type alloys.
- the rate of silicon, solidification rates and grain refinement lead to macroscopic Mg 2 Si precipitates whose size and morphology facilitate dissolution during heat treatment.
- FIG. 1 shows a foundry microstructure, without manganese, precipitated "in needles", type ⁇
- FIG. 2 shows the monostructure with manganese, precipitated "in Chinese writing", type a.
- FIGS. 3 and 4 the copper content is greater than 0.40%, which results in the presence of Al 2 Cu precipitates.
- FIG. 4 shows an example where the AlFeMnSi and Mg 2 Si precipitations can be observed surrounded. precipitates Al 2 Cu.
- FIG. 5 shows a copper content of between 0.20% and 0.40%, according to the invention, showing an absence of Al 2 Cu precipitates
Abstract
Description
Claims
Priority Applications (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
PL16703341T PL3250722T3 (en) | 2015-01-29 | 2016-01-14 | Process for obtaining a low silicon aluminium alloy part |
RS20181215A RS57888B1 (en) | 2015-01-29 | 2016-01-14 | Process for obtaining a low silicon aluminium alloy part |
HRP20181682TT HRP20181682T1 (en) | 2015-01-29 | 2018-10-16 | Process for obtaining a low silicon aluminium alloy part |
Applications Claiming Priority (2)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
FR1550700A FR3032204B1 (en) | 2015-01-29 | 2015-01-29 | ALUMINUM LOW SILICON ALLOY PIECE |
PCT/FR2016/050069 WO2016120541A1 (en) | 2015-01-29 | 2016-01-14 | Process for obtaining a low silicon aluminium alloy part |
Publications (2)
Publication Number | Publication Date |
---|---|
EP3250722A1 true EP3250722A1 (en) | 2017-12-06 |
EP3250722B1 EP3250722B1 (en) | 2018-09-12 |
Family
ID=52779906
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP16703341.4A Active EP3250722B1 (en) | 2015-01-29 | 2016-01-14 | Process for obtaining a low silicon aluminium alloy part |
Country Status (21)
Country | Link |
---|---|
US (1) | US20180002788A1 (en) |
EP (1) | EP3250722B1 (en) |
JP (1) | JP6768677B2 (en) |
KR (1) | KR20170107458A (en) |
CN (1) | CN107208197B (en) |
AU (1) | AU2016211088B2 (en) |
BR (1) | BR112017016024B1 (en) |
CA (1) | CA2973937A1 (en) |
DK (1) | DK3250722T3 (en) |
ES (1) | ES2689908T3 (en) |
FR (1) | FR3032204B1 (en) |
HR (1) | HRP20181682T1 (en) |
HU (1) | HUE039737T2 (en) |
MA (1) | MA41422A (en) |
MX (1) | MX2017009828A (en) |
PL (1) | PL3250722T3 (en) |
PT (1) | PT3250722T (en) |
RS (1) | RS57888B1 (en) |
RU (1) | RU2700218C2 (en) |
TR (1) | TR201815694T4 (en) |
WO (1) | WO2016120541A1 (en) |
Families Citing this family (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JP2022142180A (en) * | 2021-03-16 | 2022-09-30 | 本田技研工業株式会社 | Processing method of aluminum alloy, and processed article of aluminum alloy |
JP2022142163A (en) * | 2021-03-16 | 2022-09-30 | 本田技研工業株式会社 | Processing method of aluminum alloy, and processed article of aluminum alloy |
Family Cites Families (12)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE119365T1 (en) * | 1983-03-14 | 1985-03-07 | Thomas Di Saint Chamond Serio | METHOD AND DEVICE FOR PRODUCING PIECES FROM ALUMINUM OR ALUMINUM ALLOY AND PIECES OBTAINED IN THIS WAY. |
US5571347A (en) * | 1994-04-07 | 1996-11-05 | Northwest Aluminum Company | High strength MG-SI type aluminum alloy |
US20020170635A1 (en) * | 1998-05-04 | 2002-11-21 | Diserio Emile-Thomas | Process for manufacturing aluminum alloys and aluminium castings |
EP0987344B1 (en) * | 1998-08-25 | 2004-11-17 | Kabushiki Kaisha Kobe Seiko Sho | High strength aluminium alloy forgings |
RU2163939C1 (en) * | 1999-08-09 | 2001-03-10 | Государственное предприятие "Всероссийский научно-исследовательский институт авиационных материалов" | Aluminum-base alloy, method of production of semifinished products and article from this alloy |
JP2002302728A (en) * | 2001-04-09 | 2002-10-18 | Hoei Kogyo Kk | Aluminum alloy for casting and forging, aluminum cast and forged article, and production method therefor |
FR2827306B1 (en) * | 2001-07-10 | 2004-10-22 | Pechiney Aluminium | HIGH DUCTILITY ALUMINUM ALLOY FOR PRESSURE CASTING |
PL374938A1 (en) * | 2002-10-01 | 2005-11-14 | Asahi Tec Corporation | Aluminum alloy for casting-forging, aluminum cast/forged article, and method for manufacture thereof |
DE102004022817A1 (en) * | 2004-05-08 | 2005-12-01 | Erbslöh Ag | Decorative anodizable, easily deformable, mechanically highly loadable aluminum alloy, process for its production and aluminum product made from this alloy |
US20080060723A1 (en) * | 2006-09-11 | 2008-03-13 | Gm Global Technology Operations, Inc. | Aluminum alloy for engine components |
WO2009059593A2 (en) * | 2007-11-08 | 2009-05-14 | Ksm Castings Gmbh | CAST Al/Si ALLOYS |
CN101643869B (en) * | 2009-09-04 | 2011-04-06 | 河池学院 | High strength automobile aluminium alloy wheel rim |
-
2015
- 2015-01-29 FR FR1550700A patent/FR3032204B1/en not_active Expired - Fee Related
-
2016
- 2016-01-14 US US15/544,213 patent/US20180002788A1/en not_active Abandoned
- 2016-01-14 CA CA2973937A patent/CA2973937A1/en not_active Abandoned
- 2016-01-14 PT PT16703341T patent/PT3250722T/en unknown
- 2016-01-14 KR KR1020177020845A patent/KR20170107458A/en not_active Application Discontinuation
- 2016-01-14 TR TR2018/15694T patent/TR201815694T4/en unknown
- 2016-01-14 DK DK16703341.4T patent/DK3250722T3/en active
- 2016-01-14 AU AU2016211088A patent/AU2016211088B2/en active Active
- 2016-01-14 BR BR112017016024-2A patent/BR112017016024B1/en active IP Right Grant
- 2016-01-14 EP EP16703341.4A patent/EP3250722B1/en active Active
- 2016-01-14 ES ES16703341.4T patent/ES2689908T3/en active Active
- 2016-01-14 RS RS20181215A patent/RS57888B1/en unknown
- 2016-01-14 PL PL16703341T patent/PL3250722T3/en unknown
- 2016-01-14 CN CN201680007900.6A patent/CN107208197B/en active Active
- 2016-01-14 MX MX2017009828A patent/MX2017009828A/en unknown
- 2016-01-14 RU RU2017126680A patent/RU2700218C2/en active
- 2016-01-14 MA MA041422A patent/MA41422A/en unknown
- 2016-01-14 WO PCT/FR2016/050069 patent/WO2016120541A1/en active Application Filing
- 2016-01-14 JP JP2017540119A patent/JP6768677B2/en active Active
- 2016-01-14 HU HUE16703341A patent/HUE039737T2/en unknown
-
2018
- 2018-10-16 HR HRP20181682TT patent/HRP20181682T1/en unknown
Also Published As
Publication number | Publication date |
---|---|
CN107208197B (en) | 2019-11-05 |
RU2700218C2 (en) | 2019-09-13 |
HUE039737T2 (en) | 2019-01-28 |
JP6768677B2 (en) | 2020-10-14 |
MA41422A (en) | 2017-12-06 |
FR3032204B1 (en) | 2019-08-09 |
BR112017016024B1 (en) | 2021-10-19 |
EP3250722B1 (en) | 2018-09-12 |
PT3250722T (en) | 2018-10-25 |
WO2016120541A1 (en) | 2016-08-04 |
RU2017126680A3 (en) | 2019-05-24 |
AU2016211088B2 (en) | 2020-05-21 |
RS57888B1 (en) | 2019-01-31 |
BR112017016024A2 (en) | 2018-03-20 |
RU2017126680A (en) | 2019-01-28 |
US20180002788A1 (en) | 2018-01-04 |
FR3032204A1 (en) | 2016-08-05 |
JP2018507324A (en) | 2018-03-15 |
KR20170107458A (en) | 2017-09-25 |
DK3250722T3 (en) | 2018-11-05 |
MX2017009828A (en) | 2018-02-09 |
CA2973937A1 (en) | 2016-08-04 |
AU2016211088A1 (en) | 2017-08-17 |
PL3250722T3 (en) | 2019-03-29 |
HRP20181682T1 (en) | 2018-12-14 |
ES2689908T3 (en) | 2018-11-16 |
TR201815694T4 (en) | 2018-11-21 |
CN107208197A (en) | 2017-09-26 |
Similar Documents
Publication | Publication Date | Title |
---|---|---|
US9775647B2 (en) | Magnesium alloy | |
EP2516687B1 (en) | Casting made from copper containing aluminium alloy with high mechanical strength and hot creep | |
FR2818288A1 (en) | METHOD OF MANUFACTURING AN AL-Si ALLOY SAFETY PART | |
EP2074237B1 (en) | Process for manufacturing hot-forged parts made of a magnesium alloy | |
JP4328321B2 (en) | Piston for internal combustion engine | |
EP3250722B1 (en) | Process for obtaining a low silicon aluminium alloy part | |
EP2421996B1 (en) | Free-machining aa 6xxx aluminum alloy | |
FR2808536A1 (en) | Production of a semi-molten billet of aluminum alloy for use as a transport unit by introducing a work distortion by cold forging | |
JP6385683B2 (en) | Al alloy casting and manufacturing method thereof | |
JP2010000514A (en) | Method for producing magnesium alloy member | |
Bolouri et al. | Characteristics of thixoformed A356 aluminum thin plates with microchannels | |
WO2018061540A1 (en) | HOT EXTRUSION-MOLDING METHOD FOR Ni-BASED SUPER HEAT-RESISTANT ALLOY AND PRODUCTION METHOD FOR Ni-BASED SUPER HEAT-RESISTANT ALLOY EXTRUSION MATERIAL | |
KR20190030296A (en) | Methods of treating aluminum alloy | |
Wang et al. | Microstructure evolution and mechanical properties of ZK60 magnesium alloy produced by SSTT and RAP route in semi-solid state | |
Trifonov et al. | Liquid forging processing of automobile wheels | |
JP5856764B2 (en) | Hypereutectic aluminum-silicon alloy rolled sheet molded product and method for producing the same | |
JP2007308780A (en) | Method for controlling structure of magnesium alloy, magnesium alloy with controlled structure, and wheel for vehicle | |
JP2018070899A (en) | Hypereutectic Al-Mn Aluminum Alloy Casting Material and Method for Producing the Same | |
EP3277451A1 (en) | Sand shell-moulding method for the production of a part for use in the automotive and aeronautics fields | |
JP2022172630A (en) | Semi-solidifying/molding method | |
JP2001240929A (en) | Aluminum wheel and its production method |
Legal Events
Date | Code | Title | Description |
---|---|---|---|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE INTERNATIONAL PUBLICATION HAS BEEN MADE |
|
PUAI | Public reference made under article 153(3) epc to a published international application that has entered the european phase |
Free format text: ORIGINAL CODE: 0009012 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE |
|
17P | Request for examination filed |
Effective date: 20170710 |
|
AK | Designated contracting states |
Kind code of ref document: A1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
AX | Request for extension of the european patent |
Extension state: BA ME |
|
DAX | Request for extension of the european patent (deleted) | ||
RAV | Requested validation state of the european patent: fee paid |
Extension state: MA Effective date: 20170823 |
|
GRAP | Despatch of communication of intention to grant a patent |
Free format text: ORIGINAL CODE: EPIDOSNIGR1 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: GRANT OF PATENT IS INTENDED |
|
INTG | Intention to grant announced |
Effective date: 20180531 |
|
GRAS | Grant fee paid |
Free format text: ORIGINAL CODE: EPIDOSNIGR3 |
|
GRAA | (expected) grant |
Free format text: ORIGINAL CODE: 0009210 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: THE PATENT HAS BEEN GRANTED |
|
AK | Designated contracting states |
Kind code of ref document: B1 Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR |
|
REG | Reference to a national code |
Ref country code: GB Ref legal event code: FG4D Free format text: NOT ENGLISH |
|
REG | Reference to a national code |
Ref country code: CH Ref legal event code: EP |
|
REG | Reference to a national code |
Ref country code: IE Ref legal event code: FG4D Free format text: LANGUAGE OF EP DOCUMENT: FRENCH |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R096 Ref document number: 602016005577 Country of ref document: DE |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: REF Ref document number: 1040671 Country of ref document: AT Kind code of ref document: T Effective date: 20181015 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: TUEP Ref document number: P20181682 Country of ref document: HR |
|
REG | Reference to a national code |
Ref country code: RO Ref legal event code: EPE |
|
REG | Reference to a national code |
Ref country code: NL Ref legal event code: FP |
|
REG | Reference to a national code |
Ref country code: PT Ref legal event code: SC4A Ref document number: 3250722 Country of ref document: PT Date of ref document: 20181025 Kind code of ref document: T Free format text: AVAILABILITY OF NATIONAL TRANSLATION Effective date: 20181004 |
|
REG | Reference to a national code |
Ref country code: DK Ref legal event code: T3 Effective date: 20181022 Ref country code: NO Ref legal event code: T2 Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: ES Ref legal event code: FG2A Ref document number: 2689908 Country of ref document: ES Kind code of ref document: T3 Effective date: 20181116 |
|
REG | Reference to a national code |
Ref country code: SE Ref legal event code: TRGR |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: T1PR Ref document number: P20181682 Country of ref document: HR |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20181218 Year of fee payment: 4 |
|
REG | Reference to a national code |
Ref country code: LT Ref legal event code: MG4D |
|
REG | Reference to a national code |
Ref country code: HU Ref legal event code: AG4A Ref document number: E039737 Country of ref document: HU |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: FI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 Ref country code: LT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: AL Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 Ref country code: LV Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: SK Ref legal event code: T3 Ref document number: E 29123 Country of ref document: SK |
|
REG | Reference to a national code |
Ref country code: GR Ref legal event code: EP Ref document number: 20180403574 Country of ref document: GR Effective date: 20190404 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: IS Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20190112 Ref country code: EE Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
VSFP | Annual fee paid to validation state [announced via postgrant information from national office to epo] |
Ref country code: MA Payment date: 20190110 Year of fee payment: 4 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: SM Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: DE Ref legal event code: R097 Ref document number: 602016005577 Country of ref document: DE |
|
PLBE | No opposition filed within time limit |
Free format text: ORIGINAL CODE: 0009261 |
|
STAA | Information on the status of an ep patent application or granted ep patent |
Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT |
|
26N | No opposition filed |
Effective date: 20190613 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MC Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 Ref country code: SI Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20191218 Year of fee payment: 5 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MT Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: AT Ref legal event code: UEP Ref document number: 1040671 Country of ref document: AT Kind code of ref document: T Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20210107 Year of fee payment: 6 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: CY Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
VS25 | Lapsed in a validation state [announced via postgrant information from nat. office to epo] |
Ref country code: MA Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20211228 Year of fee payment: 7 |
|
PG25 | Lapsed in a contracting state [announced via postgrant information from national office to epo] |
Ref country code: MK Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT Effective date: 20180912 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20221229 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: RS Payment date: 20221223 Year of fee payment: 8 Ref country code: NO Payment date: 20221228 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PL Payment date: 20221220 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: RO Payment date: 20230103 Year of fee payment: 8 Ref country code: FR Payment date: 20230125 Year of fee payment: 8 Ref country code: ES Payment date: 20230206 Year of fee payment: 8 Ref country code: CH Payment date: 20230130 Year of fee payment: 8 Ref country code: AT Payment date: 20221220 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: TR Payment date: 20230110 Year of fee payment: 8 Ref country code: SE Payment date: 20230117 Year of fee payment: 8 Ref country code: IT Payment date: 20230111 Year of fee payment: 8 Ref country code: HU Payment date: 20221217 Year of fee payment: 8 Ref country code: GB Payment date: 20230123 Year of fee payment: 8 Ref country code: DE Payment date: 20230112 Year of fee payment: 8 Ref country code: BE Payment date: 20230117 Year of fee payment: 8 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: SK Payment date: 20231220 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: GR Payment date: 20231219 Year of fee payment: 9 |
|
REG | Reference to a national code |
Ref country code: HR Ref legal event code: ODRP Ref document number: P20181682 Country of ref document: HR Payment date: 20231221 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: NL Payment date: 20231229 Year of fee payment: 9 Ref country code: LU Payment date: 20231227 Year of fee payment: 9 Ref country code: IE Payment date: 20231220 Year of fee payment: 9 Ref country code: HR Payment date: 20231221 Year of fee payment: 9 Ref country code: DK Payment date: 20231228 Year of fee payment: 9 Ref country code: CZ Payment date: 20231219 Year of fee payment: 9 Ref country code: BG Payment date: 20231221 Year of fee payment: 9 Ref country code: PT Payment date: 20231218 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: PL Payment date: 20231219 Year of fee payment: 9 |
|
PGFP | Annual fee paid to national office [announced via postgrant information from national office to epo] |
Ref country code: ES Payment date: 20240207 Year of fee payment: 9 |