CN109415780B - 6xxx series aluminum alloy forging blank and manufacturing method thereof - Google Patents
6xxx series aluminum alloy forging blank and manufacturing method thereof Download PDFInfo
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- CN109415780B CN109415780B CN201780032491.XA CN201780032491A CN109415780B CN 109415780 B CN109415780 B CN 109415780B CN 201780032491 A CN201780032491 A CN 201780032491A CN 109415780 B CN109415780 B CN 109415780B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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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
- C22C21/06—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
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- 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
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Abstract
The invention relates to a hot rolled semi-finished 6 xxx-series aluminum alloy forging blank having a thickness in the range of from 2mm to 30mm and having a composition in wt.%: 0.65% -1.4% Si, 0.60% -0.95% Mg, 0.40% -0.80% Mn, 0.04% -0.28% Cu, at most 0.5% Fe, at most 0.18% Cr, at most 0.20% Zr, at most 0.15% Ti, at most 0.25% Zn, impurities, each < 0.05%, a total < 0.2%, balance aluminum, and wherein the hot rolled semi-finished 6 xxx-series aluminum alloy forging blank has a substantially unrecrystallized microstructure. The invention also relates to a method of manufacturing such a 6xxx series hot rolled aluminum alloy forging blank. Furthermore, the invention relates to a method of forging a shaped product from a6 xxx-series aluminium alloy forging blank.
Description
Technical Field
The present invention relates to a 6xxx series aluminum alloy forging blank. The invention also relates to a method for manufacturing the 6xxx series aluminum alloy forging blank. Furthermore, the invention relates to a method of hot forming a shaped product made from said 6xxx series aluminium alloy forging blank, in particular by forging. A 6xxx series aluminum alloy material may be used in the manufacture of forged automotive structural members.
Background
Several 6xxx series aluminum alloys are known in the art, and these 6xxx series aluminum alloys are extruded as a feedstock for subsequent forging operations at high temperatures into various structural components.
An aluminum alloy often used for the manufacture of wrought products is alloy AA6082, registered at the american aluminum Association (alumium Association), having the following composition in wt.%:
the balance impurities and aluminum. Wrought products made from AA6082 alloy in the T6 temper have high mechanical properties.
Another alloy used to make forgings is AA6182 having the following composition in wt.%:
the balance impurities and aluminum.
Patent document EP-2644725-B1(Kobe) discloses a production process of an aluminum alloy forged material comprising (in wt.%): 0.6-1.2% Mg, 0.7-1.5% Si, 0.1-0.5% Fe, 0.01-0.1% Ti, 0.3-1.0% Mn, one or both of 0.1-0.4% Cr and 0.05-0.2% Zr, less than 0.1% Cu, less than 0.05% Zn, the balance being aluminum and unavoidable impurities, the process comprising the steps of: casting an ingot of this alloy, extruding the ingot at a temperature in the range of 450 ℃ to 540 ℃ to provide a forging stock, heating the extruded forging stock at 500 ℃ to 560 ℃ for more than 0.75 hour, forging the forging stock into a desired shape at a temperature of 450 ℃ to 560 ℃, followed by subjecting the forged material to solution heat treatment and quenching and artificial aging.
Patent document WO-2015/146654-a1(Kobe) discloses a process for producing an aluminum alloy forged material containing (in wt.%): 0.70-1.50% Mg, 0.80-1.30% Si, 0.30-0.90% Cu, 0.10-0.40% Fe, 0.005-0.15% Ti, and optionally one or more elements selected from 0.10-0.60% Mn, 0.10-0.45% Cr and 0.05-0.30% Zr, the balance being aluminum and unavoidable impurities, the production process comprising the steps of: casting an ingot, extruding the ingot to provide a forging stock, forging the forging stock into a desired shape at an elevated temperature, followed by solution heat treating the forged material and quenching and artificial aging.
Disclosure of Invention
It is an object of the present invention to provide a 6xxx series aluminum alloy forging raw material for producing a forged product having a good balance in strength and ductility. It is another object of the present invention to provide a method of producing a 6xxx series aluminum alloy forging raw material for producing a forged product having a good balance in strength and ductility.
Detailed Description
It should be understood that, unless otherwise indicated, aluminum alloy designations and condition designations (temper designations) refer to the aluminum Association designations in "aluminum Standards and Data and the Registration Records" published by the aluminum Association of the united states in 2016 and are well known to those skilled in the art. The status code is specified in european standard EN 515.
For any description of an alloy composition or preferred alloy composition, all percentages mentioned are weight percentages unless otherwise indicated.
As used herein, the terms "at most" and "at most about" expressly include, but are not limited to, the possibility of zero weight percent of the particular alloy component to which they refer. For example, up to 0.25% Zn may comprise a Zn-free alloy.
As used herein, the term "about" when used to describe a compositional range or amount of an alloy addition means that the actual amount of the alloy addition may differ from the nominal expected amount due to factors such as standard process variations as understood by those skilled in the art.
This and other objects and further advantages are met or exceeded by the present invention by providing a hot rolled semi-finished 6 xxx-series aluminium alloy forging blank suitable for the manufacture of automotive structural parts and having a final thickness in the range of from 2mm to 30mm, preferably in the range of from 2mm to 20mm, more preferably in the range of from 2mm to 15mm, and having the following composition in wt.%,
impurities, each < 0.05%, total < 0.2%, balance aluminum,
and wherein, in a hot rolled condition, the hot rolled semi-finished 6xxx series aluminum alloy forging blank has a substantially unrecrystallized microstructure.
The delicate balance between alloying constituents and microstructure in the hot rolled state allows the subsequent production of forged products with a good balance in strength and ductility. The use of hot rolled stock allows for the production of wider forged products than the use of extruded stock. Furthermore, the manufacture of rolling stock is a robust production process that can produce large volumes of forging stock in a more cost-effective manner than extrusion processes that require dedicated extrusion dies and in which only billets (billets) of limited size can be processed. Furthermore, the rolling stock provides a more homogeneous microstructure in the product and avoids the occurrence of so-called profile hot spots (hot-spots) which may frequently occur in extrusion processes, for example due to an unbalanced melting of the eutectic phase caused by temperature fluctuations across the profile in the extrusion process.
By substantially unrecrystallized microstructure we mean that more than 85%, preferably more than 90%, more preferably more than 95% of the microstructure is substantially unrecrystallized throughout the thickness of the hot rolled product.
Purposeful addition of Mg and Si due to elemental Si and Mg formed in the coexistence of Mg2Precipitation hardening of Si strengthens the aluminum alloy. In order to provide a sufficient level of strength in the final product, the Si content should be at least 0.65%, preferably at least 0.8%, more preferably at least 0.90%. The preferable upper limit of the Si content is 1.30%, more preferably 1.25%.
For essentially the same reasons as the Si content, the Mg content should be at least 0.60%, preferably at least 0.65%, more preferably at least 0.70%, to provide sufficient strength to the final product. The preferable upper limit of the Mg content is 0.85%, more preferably 0.80%.
The addition of Mn serves to provide the desired microstructure in the alloy product and increases strength and ductility. At least 0.40%, preferably at least 0.50%, more preferably at least 0.55% Mn should be present. The Mn content should not exceed 0.80%, preferably not exceed 0.70%, more preferably not exceed 0.65%, to provide a suitable balance in strength, toughness and ductility.
The purposeful addition of Cu is an essential feature of the present invention in order to achieve the desired balance of mechanical and physical properties in the final product. Preferably, the aluminum alloy has at least 0.08% Cu, more preferably at least 0.12%. The preferred upper limit of the Cu content is 0.27%, more preferably at most 0.24%.
It is important that the Fe content in the aluminum alloy product should not exceed about 0.5%, preferably should not exceed about 0.35%, in order to maintain a balance of properties. Too high an amount of Fe may adversely affect the toughness and ductility of the final product. The upper limit of the Fe content is more preferably 0.30%. Lower Fe content contributes to the ductility of the alloy product. The lower limit of the Fe content is about 0.1%, more preferably about 0.15%. Too low a Fe content makes the aluminium alloy product very expensive.
In order to control the grain structure during the hot rolling operation and during the subsequent hot forming operation, it is preferred to purposefully add Zr alone or Cr alone, or a combination of Zr and Cr.
In the embodiment, the addition amount of Zr is preferably in the range of 0.05% to 0.20%. The preferred lower limit of the Zr content is 0.06%. A preferred upper limit for Zr content is about 0.16%.
In the examples, the content of Cr should be in the range of 0.06% to 0.18%. A preferred upper limit for the Cr content is about 0.14%, preferably about 0.12%, and more preferably 0.09%.
In another embodiment, Zr and Cr are added in combination, the alloying elements Cr and Zr are each in the ranges as described herein, and the sum of the combined addition amounts of Zr + Cr does not exceed 0.30%, preferably does not exceed 0.25%. The combined addition of Zr and Cr is most effective in suppressing grain growth and controlling grain size in the final forged product.
Zinc is an impurity element which may be tolerated up to about 0.25%, preferably up to 0.10%, and more preferably as low as possible, for example below 0.05%.
Titanium may be added to the aluminum alloy product during casting of the alloy ingot for the purpose of a grain refiner. The amount of Ti added should not exceed about 0.15%, preferably should not exceed 0.1%. A preferred lower limit of the Ti addition amount is 0.01%, and a preferred upper limit of Ti is generally 0.05%, and Ti may be added as a separate element or, as known in the art, together with boron and carbon used as a casting aid for grain size control.
Unavoidable impurities may be present, each up to about 0.05% and the total up to about 0.20%, with the balance being aluminum.
In a preferred embodiment, the aluminum alloy product has the following composition in wt.%,
impurities, each < 0.05%, total < 0.2%, balance aluminum, and having a preferred narrower range as described and claimed herein.
In another aspect of the present invention, it relates to a method of manufacturing a hot-rolled semi-finished 6 xxx-series aluminum alloy forging blank according to the present invention, comprising the steps of:
a. casting to form an ingot of the hot rolled feedstock,
b. homogenizing the cast ingot at a temperature in the range of 460 ℃ to 580 ℃,
c. hot rolling in one or more rolling passes to a final gauge (gauge) in the range of 2 to 30mm and wherein the hot rolling mill exit temperature is in the range of 200 ℃ to 360 ℃.
The delicate balance between alloying constituents and providing a substantially unrecrystallized microstructure in the hot rolled state allows for the production of forged products with a good balance of strength and ductility. The use of hot rolled stock allows for the production of wider forged products than the use of extruded stock. Furthermore, the manufacture of rolling stock is a robust production process that can produce large volumes of forging stock in a more cost-effective manner than extrusion processes that require dedicated extrusion dies and in which only billets of limited size can be processed. Furthermore, the rolling stock provides a more uniform microstructure in the product and avoids the occurrence of so-called profile hot spots, which may frequently occur in extrusion processes, for example, due to an unbalanced melting of eutectic phases, which is caused by temperature fluctuations across the profile in the extrusion process.
The aluminum alloy may be provided as an ingot or slab to be manufactured as a hot rolled stock using casting techniques conventional in the art of casting products (e.g., DC casting, EMC casting, EMS casting), and preferably has an ingot thickness in the range of about 220mm or greater (e.g., 300mm or 350 mm). In the embodiment, a thin gauge slab having a thickness of at most about 40mm, which is produced by continuous casting such as a belt casting machine or a roll casting machine, may also be used. Grain refiners such as those containing titanium and boron or titanium and carbon may also be used, as is well known in the art. After casting the hot rolled raw material, the as-cast ingot is usually peeled to remove segregation zones (segregation zones) near the casting surface of the ingot.
Homogenization should be carried out at temperatures above 460 ℃. If the homogenization temperature is below 460 ℃, the reduction of ingot segregation and homogenization may be insufficient. This results in Mg contributing to the strength2The dissolution of the Si component is insufficient, and the formability may be reducedAnd (4) sex. Preferably, the homogenization is carried out at a temperature above 480 ℃. The homogenization temperature should not exceed 570 ℃ and preferably it does not exceed 560 ℃. More preferably, homogenization is carried out at a temperature in the range of 480 ℃ to 520 ℃. In the presence of a high volume fraction of Mn, Zr and Cr-containing dispersions, homogenization at temperatures below 520 ℃ is preferred in order to avoid any coarsening of these particles.
The heating rates that can be used are those conventional in the art.
The soaking time for homogenization should be at least about 2 hours, and more preferably, at least about 4 hours. The preferred upper limit for the homogenizing soak time is about 24 hours, and more preferably 15 hours.
In an example, the cast ingot was homogenized at a temperature and soaking time as described herein, then quenched to below 100 ℃ using a water quench system to ensure a high level of dissolution of the component particles, and then reheated to the hot mill inlet temperature.
In the next processing step, the ingot is hot rolled in one or more rolling steps to final gauge in the range of 2mm to 30mm, preferably 2mm to 20mm, more preferably 2mm to 15 mm. The method according to the invention avoids the need for further gauge reduction by cold rolling. The hot rolling process is carefully controlled so that the hot mill exit temperature is in the range of 200 ℃ to 360 ℃, preferably 230 ℃ to 280 ℃ to ensure that the hot rolled feedstock has a substantially unrecrystallized microstructure. The hot rolling mill outlet temperature in this temperature range suppresses the temperature of the molten steel such as Si and Mg2Coarse precipitation of secondary phases, such as Si and AlMgCu, enables a balance of high strength and good ductility to be achieved in the final forged product. At too high hot mill exit temperatures, the grain size in the final forged product is too coarse, e.g., the average grain size exceeds 90 microns.
On a preferred basis, the hot mill inlet temperature is in the range of 400 ℃ to 550 ℃, preferably 435 ℃ to 535 ℃, more preferably below 500 ℃ in order to achieve the desired hot mill outlet temperature.
After the hot rolling operation, the feedstock may be coiled or cut to length.
Thereafter, the final gauge forging stock may be processed into the desired shaped product, particularly into automotive structural parts, by a hot forming process using the following processing steps:
d. the final gauge hot rolled semi-finished 6xxx series aluminum alloy forging stock is solution heat treated ("SHT") and preferably followed by a quenching operation to a temperature below 70 ℃. Solution heat treatment is typically performed in the same temperature range as homogenization of the cast ingot, i.e., in the range of 460 ℃ to 560 ℃, but typically with a short soak time of up to about 5 hours (e.g., about 0.5 hours or about 1 hour). In a preferred embodiment, the temperature of the solution heat treatment is in the range of 520 ℃ to 560 ℃, and preferably just above Mg2Solidus temperature of Si and Si phases. After solution heat treatment, the material is preferably rapidly cooled or quenched to below 70 ℃.
e. Optionally reheating the solution heat treated material to a hot forming temperature or, alternatively, not cooling the solution heat treated material to ambient temperature but directly hot forming the solution heat treated material by minimizing any heat loss in the transfer from the solution heat treatment furnace to the hot forming press;
f. hot forming into the desired shaped product, preferably by forging (e.g. swaging), and wherein preferably the forging die is preheated, and preferably the forging operation is carried out with the feedstock at a temperature in the range of 400 ℃ to 560 ℃, and preferably rapid cooling using water quenching. This results in a substantially recrystallized microstructure of the forged product. Optionally, the wrought product is naturally aged at room temperature for up to 30 hours, and preferably 5 hours to 30 days, followed by artificial aging;
g. the thermoformed shaped product is artificially aged, preferably by applying one or more aging steps, to reach the final properties, and wherein at least one aging step comprises holding the thermoformed shaped product at a temperature between 150 ℃ and 210 ℃ for a period of time of 0.5 to 20 hours, and preferably for a period of time of 0.5 to 10 hours.
In an embodiment, the hot formed or forged product is preferably subjected to Solution Heat Treatment (SHT) at a temperature of about 460 ℃ to 560 ℃, preferably about 500 ℃ to 560 ℃, for 20 minutes to 8 hours, preferably 20 minutes to 2 hours, and quenched to less than 70 ℃ prior to artificial aging, which artificially aging brings the product to a T6X state after aging by applying one or more aging steps, and wherein at least one aging step comprises holding the hot formed shaped product at a temperature between 150 ℃ and 210 ℃ for a period of time of 0.5 hours to 15 hours. For example, at 175 ℃ for 8 hours, or at 160 ℃ for 10 hours.
The present invention is intended to encompass several alternative production routes for manufacturing forged products using hot rolled raw materials, for example, a non-limiting production route comprising at least the following sequence of processing steps:
route a: SHT of hot rolled stock, forging, optional quenching of the forged product, and artificial aging.
Route B: hot rolling stock SHT, forging at a temperature range of SHT, quenching of the forged product, and artificial aging.
Route C: hot rolling the feedstock SHT, quenching, reheating to forging temperature, forging, optional quenching of the forged product, and artificial aging.
Route D: hot rolling stock SHT, quenching, reheating to forging temperature, forging, optional quenching of the forged product, quenching of the SHT and SHT products, and artificial aging.
In another aspect the present invention relates to a forged structural member having a substantially recrystallized microstructure made from a hot rolled semi-finished 6 xxx-series aluminium alloy forging blank or obtained by a method of manufacturing a forged product using such a hot rolled 6 xxx-series forging blank. By substantially recrystallized microstructure we mean that more than 90%, preferably more than 95%, more preferably more than 97% of the microstructure is substantially recrystallized throughout the thickness of the forged product.
In the examples, the forged product in the T6x temper has an equivalent bending angle in the LT direction of 60 ° or more, preferably 70 ° or more, more preferably 80 ° or more, when measured on a 2mm plate material according to VDA238-100 of 12 months 2010. The bend angle indicates the ductility of the forged material, with higher bend angles indicating higher ductility. For applications of forged products in which high-speed impacts, in particular in the event of a vehicle collision, should be tolerated, a high ductility is desired as an engineering parameter. The forged product in this state has a tensile yield strength of at least 330MPa, and preferably at least 335 MPa.
In an embodiment, the forged product in the T6x temper has a tensile yield strength in the L direction of at least 350MPa, and preferably at least 360 MPa.
The forged product may be used as a structural member on an automotive structural member as well as in a non-automotive structural member.
The structural member of the automobile comprises a side anti-collision beam, a B column inner member, a B column outer member, an A column outer member, a channel reinforcement, a door belt reinforcement and a hinge reinforcement.
Furthermore, the present invention relates to the production of a forged product via the processing steps d.to g. by the preferred embodiments described herein, using cast, homogenized hot rolled raw material (i.e. the resulting intermediate product obtained by the processing steps a.to c.).
The invention is not limited to the embodiments described in the foregoing, but may be varied widely within the scope of the invention as defined by the following claims.
Claims (28)
1. A hot rolled semi-finished 6 xxx-series aluminum alloy forging blank having a thickness in the range of from 2mm to 30mm and having a composition, in wt.%:
impurities, each < 0.05%, total < 0.2%, balance aluminum,
and in that the hot rolled semi-finished 6xxx series aluminum alloy forging blank has a substantially unrecrystallized microstructure.
2. The hot rolled semi-finished 6xxx series aluminum alloy forging blank of claim 1, wherein the Cu content is in the range of 0.08% to 0.27%.
3. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank of claim 2, wherein the Cu content is in the range of 0.12% to 0.27%.
4. The hot-rolled semi-finished 6 xxx-series aluminum alloy forging blank as claimed in any one of claims 1 to 3, wherein the Mn content is in the range of 0.50% to 0.70%.
5. The hot-rolled semi-finished 6 xxx-series aluminum alloy forging blank as claimed in any one of claims 1 to 3, wherein the Si content is in the range of 0.8% to 1.30%.
6. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank as claimed in any one of claims 1 to 3, wherein the Mg content is in the range of 0.70% to 0.90%.
7. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank of claim 6, wherein the Mg content is in the range of 0.70% to 0.85%.
8. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank as claimed in any one of claims 1 to 3, wherein the Cr content is in the range of 0.06% to 0.18%.
9. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank of claim 8, wherein the Cr content is in the range of 0.06% to 0.14%.
10. The hot-rolled semi-finished 6 xxx-series aluminum alloy forging blank as claimed in any one of claims 1 to 3, wherein the Zr content is in the range of 0.05% to 0.20%.
11. The hot rolled semi-finished 6 xxx-series aluminum alloy forging blank of claim 10, wherein the Zr content is in the range of from 0.05% to 0.16%.
12. A method of manufacturing a hot rolled semi-finished 6 xxx-series aluminum alloy forging blank as defined in any one of claims 1 to 11, comprising the steps of:
-casting an ingot forming a hot rolled feedstock and having the composition of any one of claims 1 to 11;
-homogenizing the cast ingot at a temperature in the range of 460 ℃ to 570 ℃;
-hot rolling in one or more rolling passes to a hot mill exit gauge in the range of 2 to 30mm, and wherein the hot mill exit temperature is in the range of 200 ℃ to 360 ℃.
13. The method of claim 12, wherein the hot rolling mill inlet temperature is in the range of 400 ℃ to 550 ℃.
14. The method of claim 13, wherein the hot rolling mill inlet temperature is in the range of 435 ℃ to 535 ℃.
15. The method of claim 14, wherein the hot rolling mill inlet temperature is in the range of 435 ℃ to less than 500 ℃.
16. A method of manufacturing a forged product using a hot rolled semi-finished 6 xxx-series aluminum alloy forging blank, comprising the steps of:
-solution heat treating the hot rolled semi-finished 6xxx series aluminum alloy forging blank as defined in any one of claims 12 to 15;
-hot forming into a shaped product and having a substantially recrystallized microstructure; and
-artificially ageing said shaped product.
17. The method of claim 16, wherein the shaped product is artificially aged to a T6x state.
18. The method of claim 16 or 17, wherein the hot forming is by forging.
19. The method of claim 18, wherein the hot forming is by swaging.
20. The method of claim 16 or 17, wherein the shaped product is solution heat treated after being hot formed into a shaped product but before artificial aging.
21. The method as claimed in claim 16, wherein the shaped product after artificial ageing has a bending angle of at least 60 ° when measured according to VDA238-100 on a 2mm product.
22. The method of claim 21 wherein the shaped product after artificial aging has a bend angle of at least 70 ° when measured on a 2mm product according to VDA 238-100.
23. The method of claim 21 or 22, wherein the shaped product after artificial aging is a forged product.
24. The method of claim 16 or 17, wherein the shaped product, after artificial aging, has a tensile yield strength of at least 330 MPa.
25. The method of claim 24, wherein the shaped product after artificial aging is a wrought product.
26. Use of a hot rolled semi-finished 6 xxx-series aluminum alloy forging blank having a thickness in the range of from 2mm to 30mm and having a composition in wt.%:
impurities, each < 0.05%, total < 0.2%, balance aluminum,
and wherein the hot rolled semi-finished 6 xxx-series aluminum alloy forging blank has a substantially unrecrystallized microstructure and is obtained by the method of any one of claims 12 to 15 when producing a forged product having a substantially recrystallized microstructure.
27. Use according to claim 26 of a hot rolled semi-finished 6 xxx-series aluminum alloy forging blank having a thickness in the range of from 2mm to 30mm and having a composition in wt.%:
impurities, each < 0.05%, total < 0.2%, balance aluminum,
and characterized in that the hot-rolled semi-finished 6 xxx-series aluminum alloy forging blank has a substantially unrecrystallized microstructure and is obtained by the method of any one of claims 12 to 15 when producing a forged product according to any one of claims 16 to 25.
28. Use according to claim 26 or 27, wherein the forged product is a die-forged product.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP16172448 | 2016-06-01 | ||
| EP16172448.9 | 2016-06-01 | ||
| PCT/EP2017/063109 WO2017207603A1 (en) | 2016-06-01 | 2017-05-31 | 6xxx-series aluminium alloy forging stock material and method of manufacting thereof |
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| CN109415780A CN109415780A (en) | 2019-03-01 |
| CN109415780B true CN109415780B (en) | 2021-02-23 |
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| US (1) | US20190136348A1 (en) |
| EP (1) | EP3464659B2 (en) |
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| WO (1) | WO2017207603A1 (en) |
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| CN111542627A (en) | 2017-12-21 | 2020-08-14 | 肯联铝业机床杰钦有限公司 | 6xxx aluminum alloy extrusion forging stock and manufacturing method thereof |
| US11345980B2 (en) | 2018-08-09 | 2022-05-31 | Apple Inc. | Recycled aluminum alloys from manufacturing scrap with cosmetic appeal |
| CN110129634B (en) * | 2019-05-23 | 2021-10-22 | 鼎镁新材料科技股份有限公司 | Impact-resistant high-energy-absorption high-manganese 6XXX series aluminum alloy and preparation method thereof |
| CN112553513A (en) * | 2019-09-25 | 2021-03-26 | 苹果公司 | Aesthetic aluminum alloy made from recycled aluminum scrap |
| FR3101641B1 (en) * | 2019-10-04 | 2022-01-21 | Constellium Issoire | Aluminum alloy precision sheets |
| KR20210080908A (en) * | 2019-12-23 | 2021-07-01 | 현대자동차주식회사 | Manufacturing method of an aluminum alloyand the aluminum alloy |
| EP3842561B1 (en) * | 2019-12-23 | 2022-08-17 | Novelis Koblenz GmbH | Method of manufacturing an aluminium alloy rolled product |
| CN111074087B (en) * | 2019-12-25 | 2021-07-16 | 上海友升铝业股份有限公司 | Automobile doorsill beam aluminum alloy and preparation method thereof |
| CN112430766B (en) * | 2020-11-03 | 2022-02-18 | 福建祥鑫股份有限公司 | High-strength low-yield-ratio 6-series aluminum alloy and preparation method thereof |
| CN112410628B (en) * | 2020-12-03 | 2022-04-12 | 河南永通铝业有限公司 | High-strength aluminum alloy plate for curtain wall and preparation method thereof |
| EP4275812A1 (en) * | 2022-05-13 | 2023-11-15 | TRIMET Aluminium SE | Aluminum alloy structural components, precursor material and method of manufacturing the same |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5547371A (en) * | 1978-10-02 | 1980-04-03 | Sumitomo Light Metal Ind Ltd | Manufacture of high strength aluminum alloy having excellent mechanical property in direction of wall thickness |
| CN1529763A (en) * | 2001-04-09 | 2004-09-15 | 旭技术株式会社 | Aluminium allloy for casting/forging, aluminium alloy cast/forged product and producing methods |
| EP1458898A1 (en) * | 2001-12-21 | 2004-09-22 | DaimlerChrysler AG | Hot- and cold-formed aluminium alloy |
| JP2012001756A (en) * | 2010-06-16 | 2012-01-05 | Sumitomo Light Metal Ind Ltd | HIGH-TOUGHNESS Al ALLOY FORGING MATERIAL, AND METHOD FOR PRODUCING THE SAME |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1489637A (en) * | 2000-12-21 | 2004-04-14 | �Ƹ��� | Aluminum alloy products and artificial aging method |
| JP2003277868A (en) | 2002-03-19 | 2003-10-02 | Kobe Steel Ltd | Aluminum alloy forging having excellent stress corrosion cracking resistance and stock for the forging |
| JP3766357B2 (en) | 2002-07-12 | 2006-04-12 | 株式会社神戸製鋼所 | Aluminum alloy forging material for strength member and forging material |
| JP2006274415A (en) | 2005-03-30 | 2006-10-12 | Kobe Steel Ltd | Aluminum alloy forging for high strength structural member |
| JP5180496B2 (en) * | 2007-03-14 | 2013-04-10 | 株式会社神戸製鋼所 | Aluminum alloy forging and method for producing the same |
| JP5863626B2 (en) | 2012-02-02 | 2016-02-16 | 株式会社神戸製鋼所 | Aluminum alloy forging and method for producing the same |
| JP5872443B2 (en) | 2012-03-30 | 2016-03-01 | 株式会社神戸製鋼所 | Aluminum alloy forgings for automobiles and manufacturing method thereof |
| JP5901738B2 (en) | 2014-03-27 | 2016-04-13 | 株式会社神戸製鋼所 | Aluminum alloy forging and method for producing the same |
-
2017
- 2017-05-31 EP EP17725993.4A patent/EP3464659B2/en active Active
- 2017-05-31 US US16/306,078 patent/US20190136348A1/en not_active Abandoned
- 2017-05-31 WO PCT/EP2017/063109 patent/WO2017207603A1/en unknown
- 2017-05-31 CN CN201780032491.XA patent/CN109415780B/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5547371A (en) * | 1978-10-02 | 1980-04-03 | Sumitomo Light Metal Ind Ltd | Manufacture of high strength aluminum alloy having excellent mechanical property in direction of wall thickness |
| CN1529763A (en) * | 2001-04-09 | 2004-09-15 | 旭技术株式会社 | Aluminium allloy for casting/forging, aluminium alloy cast/forged product and producing methods |
| EP1458898A1 (en) * | 2001-12-21 | 2004-09-22 | DaimlerChrysler AG | Hot- and cold-formed aluminium alloy |
| JP2012001756A (en) * | 2010-06-16 | 2012-01-05 | Sumitomo Light Metal Ind Ltd | HIGH-TOUGHNESS Al ALLOY FORGING MATERIAL, AND METHOD FOR PRODUCING THE SAME |
Non-Patent Citations (1)
| Title |
|---|
| 汽车铝合金锻件及冲挤件;赵永军 等;《轻合金加工技术》;20110430;第39卷(第4期);第1-10页 * |
Also Published As
| Publication number | Publication date |
|---|---|
| EP3464659B2 (en) | 2023-07-12 |
| CN109415780A (en) | 2019-03-01 |
| US20190136348A1 (en) | 2019-05-09 |
| WO2017207603A1 (en) | 2017-12-07 |
| EP3464659A1 (en) | 2019-04-10 |
| EP3464659B1 (en) | 2020-03-11 |
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