EP0846781B1 - Process of forming an aluminium sheet with excellent high speed superplastic formability - Google Patents
Process of forming an aluminium sheet with excellent high speed superplastic formability Download PDFInfo
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- EP0846781B1 EP0846781B1 EP95940435A EP95940435A EP0846781B1 EP 0846781 B1 EP0846781 B1 EP 0846781B1 EP 95940435 A EP95940435 A EP 95940435A EP 95940435 A EP95940435 A EP 95940435A EP 0846781 B1 EP0846781 B1 EP 0846781B1
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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
-
- 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
- C22F1/047—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 magnesium as the next major constituent
Definitions
- This invention relates to a method of producing an aluminum alloy sheet which has excellent high-speed superplastic formability, and more specifically, to a method involving an Al-Mg alloy sheet which enables superplastic forming at high strain rate of 10 -2 to 10 0 /s.
- an aluminum alloy sheet containing 2.0 to 6.0% of Mg, 0.0001 to 0.01% of Be, and 0.001 to 0.15% of Ti, with Fe and Si as impurities being controlled each at 0.2% or less and the largest grain diameter of impurity-based intermetallic compounds limited to 10 ⁇ m or less is proposed in Japanese Patent Application Laid-Open No. 72030/1992. While such a product does show an elongation of 350% or more at a strain rate of 10 -3 /s under a high-temperature deformation condition of 400°C, the elongation decreases as the forming speed increases and becomes insufficient at strain rates of 10 -2 /s or higher.
- Another aluminum alloy sheet proposed in Japanese Patent Application Laid-Open No. 318145/1992, contains 2 to 5% of Mg, 0.04 to 0.10% of Cu, as well as optional small quantities of certain transition elements, Cr, Zr, or Mn; with Si and Fe as impurities being controlled at 0.1% or less, and at 0.15% or less, respectively; while controlling the crystal grain diameter at 20 ⁇ m or less and maintaining the grain diameter and the cubic ratio of transition metal-based intermetallic compounds within certain specific ranges.
- Such an alloy sheet also has a limited application range of strain rates in the order of 10 -4 /s, and is not suitable for high strain rate superplastic forming at a higher strain rate.
- the present invention has been achieved as a result of diverse examination and exhaustive experiments concerning the relationships of superplastic formability with various alloy constituents and their quantitative combinations, in addition to those with impurity content and their distribution, as well as with crystal grain diameters of impurity-based intermetallic compounds, made in an attempt to overcome the aforementioned shortcomings of the Al-Mg superplastic aluminum alloy.
- the object of the present invention is to provide, by identifying a particular distribution and crystal grain diameter range for Al-Fe-Si compounds to be controlled based on restriction of Fe and Si as impurities, a method of producing an aluminum alloy sheet using a high strain rate superplastic forming in a forming process with a high forming speed such as at a strain rate ranging from 10 -2 to 10 0 /s.
- Mg acts to recrystallize the alloy during the high-temperature deformation.
- the content range is between 3.0 and 8.0%, below which the effect on promoting the recrystallization is insufficient while a content in excess of 8.0% acts to reduce hot workability of the material.
- Cu acts to improve the superplastic elongation of the Al-Mg alloy system.
- the content range is between 0.05 to 0.50%, where a content below 0.05% fails to give sufficient elongation while a content in excess of 0.50% acts to reduce the hot workability.
- Ti acts to turn the ingot crystals into finer grains and to provide the alloy with a better superplastic formability.
- the content range is between 0.001 to 0.1%, where a content below 0.001% will fail to give the expected effect and a content in excess of 0.1% will yield coarse compounds that hinder workability as well as ductility.
- Mn and Cr act to make recrystallized grains finer in the alloy recrystallization process that occurs during high-temperature deformation.
- the content range is below 0.10% for each, where a content in excess of 0.10% will act to increase a constituent particle whose grain diameter is 1 ⁇ m or above to decrease the superplastic formability of the alloy.
- Fe and Si are impurities each at 0.06% or less.
- These impurities form an Al-Fe-Si compound that is insoluble and prone to precipitate along the grain boundary, increasing cavities and thereby impairing the superplastic elongation.
- the Fe and Si should each be controlled at 0.05% or less. It is also noted here that up to 50 ppm of Be may be added to prevent oxidation of the molten metal, just as in the case of ordinary Al-Mg alloys.
- the Al-Fe-Si compound present in the alloy matrix gives rise to the above mentioned problem, it is better to allow as little of such a compound as possible, and, in particular, the limit in terms of number per square millimeter of an Al-Fe-Si compound having a grain diameter of 1 ⁇ m or more should be 2000 or less, since particles in excess of 2000 per square millimeter will increase cavities and thereby impair the superplastic elongation.
- the original mean crystal grain diameter of the aluminum alloy sheet it is preferrably required to regulate the original mean crystal grain diameter of the aluminum alloy sheet within a range of 25 to 200 ⁇ m. If the original mean crystal grain diameter is below 25 ⁇ m, the original crystal grains will be recreated when recrystallization occurs during high temperature deformation, making it difficult to obtain a recrystallized structure with clean crystal grains as a result of a recrystallization process to obliterate the grain boundary with precipitation of the aforementioned insoluble compounds. If the original mean crystal grain diameter exceeds 200 ⁇ m, the shearing deformation within the crystal grains becomes more prominent with increasing deformation rate, causing the crystal grains to rupture more easily, thus suppressing the superplastic elongation.
- the range of the strain rate during the forming process is between 10 -2 to 10°/s, where a rate below 10 -2 /s will cause the crystal grains to become coarser, reducing elongation, while a strain rate exceeding 10°/s creates a shearing deformation within the crystal grains causing cracks, or forms precipitation along the grain boundary, reducing elongation.
- an aluminum alloy material with the above mentioned composition is melted, cast, and homogenized according to a conventional method. It is preferable to carry out the homogenizing process at a temperature between 450 to 550°C. At temperatures below 450°C, Mg or Cu that are formed along the grain boundary or the cell boundary of the ingot by segregation will not be fully dissolved and may contribute to cracks in a subsequent hot rolling step. Conversely, at temperatures exceeding 550°C, the Al-Mg or Al-Mg-Cu crystallization products will cause a eutectic fusion thereby giving rise to cracks during the hot rolling process.
- the ingot is hot-rolled to obtain a structure suitable as a forming material. While the required starting temperature for hot rolling is between 250 to just under 400°C. If the hot rolling process is started at a temperature below 250°C, the deformation resistance is too high, making proper rolling difficult. If the rolling temperature is too high, this could alter the distribution form of the precipitation, thereby making it difficult to obtain the required crystal grain structure as well as proper distribution of precipitated compounds.
- a cold rolling is provided.
- an intermediate annealing may be provided as necessary.
- the final annealing of the cold rolled stock should be provided at a temperature between 350 to 550°C. If the annealing is performed at a temperature below 350°C, the isotropy created during the cold rolling process may not completely disappear; if higher than 550°C, a local melting may occur at the recrystallization boundary. As such, it is preferred to conduct the final annealing in a rapid annealing process such as continuous annealing.
- the Al-Fe-Si compounds present in the matrix are controlled within certain specific distribution while maintaining the crystal grain diameter within a certain specific range, resulting in such alloy structure and characteristics to produce cleaner grain boundaries with less compounds formed along these bounderies to suppress cavity formation. Recrystallized grains having an average diameter of 20 ⁇ m or less are formed during a high-temperature deformation, thereby achieving an excellent elongation of 380% or greater in high speed forming at a strain rate of 10 -2 to 10°/s in a temperature range of 350 to 550°C.
- Al-Mg based aluminum alloys having compositions as listed in Table-1 below were melted and cast into ingots via a DC casting method.
- the resultant ingots were homogenized at 530°C for 10 hours to a thickness of 30 mm, and then hot rolled at 390°C to a thickness of 4 mm.
- the sheets were subsequently cold rolled to a thickness of 2 mm and then rapidly annealed by heating rapidly to 480°C and holding at this temperature for 5 minutes.
- Specimens prepared from the test materials produced in the above process were evaluated by a tensile test at a strain rate of 10 -2 /s at 480°C.
- Table 1 lists the average crystal grain diameter for each specimen(as measured at the sheet surface), the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, and the elongation measurement results. Note here that the grain count of the compound was made using image processing.
- Al-Mg based aluminum alloys having compositions as listed in Table 2 were melted and cast into ingots in the same manner as in Examples 1, and made into 2-mm thick test materials using the same process as in Examples 1. Specimens were then evaluated in the same tensile test under the same conditions. Table 2 lists the average crystal grain diameter, the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, and the elongation measurement results.
- the average crystal grain diameter (as measured at the sheet surface) for all of these specimens was in the range of 50 to 60 ⁇ m, and the number per square millimeter of grains of the AL-Fe-Si compound having a diameter of 1 ⁇ m or above, likewise, was below 2000.
- the present invention provides a method for the production of an Al-Mg aluminum alloy sheet having excellent superplastic elongation in high speed forming such as at high strain rate of 10 -2 to 10 0 /s at a high temperature, and a superplastic forming process using this aluminum alloy sheet shortens the forming time to improve productivity.
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Description
This invention relates to a method of producing an aluminum alloy sheet which
has excellent high-speed superplastic formability, and more
specifically, to a method involving an Al-Mg alloy sheet which enables
superplastic forming at high strain rate of 10-2 to 100/s.
Based on Al-Mg alloy systems, by using a technique of
regulating recrystallization to obtain finer crystal grains,
superplastic alloys having an elongation of several hundred
percent in high temperature ranges such as that between 500
to 550°C have been developed and are being used in various
applications. However, conventional Al-Mg superplastic
alloys demonstrate the best elongation at a forming speed (i.e.
strain rate) between 10-4 to 10-3/s, at which it takes 30 to
100 minutes, for example, to form an ordinary utensil. This
is an unacceptably low productivity for a commercial
manufacturing process. Superplastic alloys that can be
formed at a much higher forming speed are therefore required.
For example, an aluminum alloy sheet containing 2.0 to
6.0% of Mg, 0.0001 to 0.01% of Be, and 0.001 to 0.15% of Ti,
with Fe and Si as impurities being controlled each at 0.2% or
less and the largest grain diameter of impurity-based
intermetallic compounds limited to 10 µm or less is proposed
in Japanese Patent Application Laid-Open No. 72030/1992.
While such a product does show an elongation of 350% or more
at a strain rate of 10-3/s under a high-temperature deformation
condition of 400°C, the elongation decreases as the forming
speed increases and becomes insufficient at strain rates of
10-2/s or higher.
Another aluminum alloy sheet, proposed in Japanese
Patent Application Laid-Open No. 318145/1992, contains 2 to
5% of Mg, 0.04 to 0.10% of Cu, as well as optional small
quantities of certain transition elements, Cr, Zr, or Mn; with
Si and Fe as impurities being controlled at 0.1% or less, and
at 0.15% or less, respectively; while controlling the crystal
grain diameter at 20 µm or less and maintaining the grain
diameter and the cubic ratio of transition metal-based
intermetallic compounds within certain specific ranges. Such
an alloy sheet also has a limited application range of strain
rates in the order of 10-4/s, and is not suitable for high strain
rate superplastic forming at a higher strain rate.
The present invention has been achieved as a result of
diverse examination and exhaustive experiments concerning the
relationships of superplastic formability with various alloy
constituents and their quantitative combinations, in addition
to those with impurity content and their distribution, as well
as with crystal grain diameters of impurity-based
intermetallic compounds, made in an attempt to overcome the
aforementioned shortcomings of the Al-Mg superplastic
aluminum alloy. In particular, the object of the present
invention is to provide, by identifying a particular
distribution and crystal grain diameter range for Al-Fe-Si
compounds to be controlled based on restriction of Fe and Si
as impurities, a method of producing an aluminum alloy sheet using a high
strain rate superplastic forming
in a forming process with a high forming speed such
as at a strain rate ranging from 10-2 to 100/s.
The invention is given by the method of claim 1 and
preferred embodiments in the dependent claims.
Referring to the significance of the alloy constituents
described in this invention and the basis of their stated
limits, first of all, Mg acts to recrystallize the alloy during
the high-temperature deformation. The content
range is between 3.0 and 8.0%, below which the effect on
promoting the recrystallization is insufficient while a
content in excess of 8.0% acts to reduce hot workability of
the material. Cu on the other hand acts to improve the
superplastic elongation of the Al-Mg alloy system. The
content range is between 0.05 to 0.50%, where a
content below 0.05% fails to give sufficient elongation while
a content in excess of 0.50% acts to reduce the hot workability.
Ti acts to turn the ingot crystals into finer grains
and to provide the alloy with a better superplastic formability.
The content range is between 0.001 to 0.1%, where
a content below 0.001% will fail to give the expected effect
and a content in excess of 0.1% will yield coarse compounds
that hinder workability as well as ductility. Further, Mn and
Cr act to make recrystallized grains finer in the alloy
recrystallization process that occurs during high-temperature
deformation. The content range is
below 0.10% for each, where a content in excess of 0.10% will
act to increase a constituent particle whose grain diameter
is 1 µm or above to decrease the superplastic formability of
the alloy.
In the present invention, it is essential to limit Fe
and Si as impurities each at 0.06% or less. These impurities
form an Al-Fe-Si compound that is insoluble and prone to
precipitate along the grain boundary, increasing cavities and
thereby impairing the superplastic elongation. Preferably,
the Fe and Si should each be controlled at 0.05% or less. It
is also noted here that up to 50 ppm of Be may be added to prevent
oxidation of the molten metal, just as in the case of ordinary
Al-Mg alloys.
Referring further to the alloy structure according to the preferred embodiments of the
invention, the Al-Fe-Si compound present in the alloy
matrix gives rise to the above mentioned problem, it is better
to allow as little of such a compound as possible, and, in
particular, the limit in terms of number per square millimeter
of an Al-Fe-Si compound having a grain diameter of 1 µm or more
should be 2000 or less, since particles in excess of 2000 per
square millimeter will increase cavities and thereby impair
the superplastic elongation.
It is preferrably required to regulate the original mean crystal
grain diameter of the aluminum alloy sheet within a range of
25 to 200 µm. If the original mean crystal grain diameter is
below 25 µm, the original crystal grains will be recreated when
recrystallization occurs during high temperature deformation,
making it difficult to obtain a recrystallized structure with
clean crystal grains as a result of a recrystallization process
to obliterate the grain boundary with precipitation of the
aforementioned insoluble compounds. If the original mean
crystal grain diameter exceeds 200 µm, the shearing
deformation within the crystal grains becomes more prominent
with increasing deformation rate, causing the crystal grains
to rupture more easily, thus suppressing the superplastic
elongation.
It is necessary to carry out a forming process for the
aluminum alloy sheet of the present invention at a temperature
between 350 to 550°C. At a temperature below 350°C, Al-Mg or
Al-Mg-Cu compounds are prone to precipitate along the grain
boundary to lower the elongation. Conversely, at a forming
temperature exceeding 550°C, the crystal grains tend to become
coarse, adversely affecting the elongation. The
range of the strain rate during the forming process is between
10-2 to 10°/s, where a rate below 10-2/s will cause the crystal
grains to become coarser, reducing elongation, while a strain
rate exceeding 10°/s creates a shearing deformation within the
crystal grains causing cracks, or forms precipitation along
the grain boundary, reducing elongation.
As a procedure for preparing the aluminum alloy sheet
in the present invention, an aluminum alloy material with the
above mentioned composition is melted, cast, and homogenized
according to a conventional method. It is preferable to carry
out the homogenizing process at a temperature between 450 to
550°C. At temperatures below 450°C, Mg or Cu that are formed
along the grain boundary or the cell boundary of the ingot by
segregation will not be fully dissolved and may contribute to
cracks in a subsequent hot rolling step. Conversely, at
temperatures exceeding 550°C, the Al-Mg or Al-Mg-Cu
crystallization products will cause a eutectic fusion thereby
giving rise to cracks during the hot rolling process.
After the homogenization process, the ingot is hot-rolled
to obtain a structure suitable as a forming material.
While the required starting temperature for hot rolling is
between 250 to just under 400°C.
If the hot rolling process is started at a temperature below
250°C, the deformation resistance is too high, making proper
rolling difficult. If the rolling temperature is too high,
this could alter the distribution form of the precipitation,
thereby making it difficult to obtain the required crystal
grain structure as well as proper distribution of precipitated
compounds.
Following the hot rolling process, a cold rolling is
provided. In addition, an intermediate annealing may be
provided as necessary. The final annealing of the cold rolled
stock should be provided at a temperature between 350 to 550°C.
If the annealing is performed at a temperature below 350°C,
the isotropy created during the cold rolling process may not
completely disappear; if higher than 550°C, a local melting
may occur at the recrystallization boundary. As such, it is
preferred to conduct the final annealing in a rapid annealing
process such as continuous annealing.
In the present invention, by restricting content of Fe
and Si as impurities in an Al-Mg alloy system and adjusting
the combination of manufacturing conditions to the combination
of the alloy constituents as described above, the Al-Fe-Si
compounds present in the matrix are controlled within certain
specific distribution while maintaining the crystal grain
diameter within a certain specific range, resulting in such
alloy structure and characteristics to produce cleaner grain
boundaries with less compounds formed along these bounderies
to suppress cavity formation. Recrystallized grains having
an average diameter of 20 µm or less are formed during a
high-temperature deformation, thereby achieving an excellent
elongation of 380% or greater in high speed forming at a strain
rate of 10-2 to 10°/s in a temperature range of 350 to 550°C.
The following describes examples of practical
applications and comparative experiments pertaining to the
present invention.
Al-Mg based aluminum alloys having compositions as
listed in Table-1 below were melted and cast into ingots via
a DC casting method. The resultant ingots were homogenized
at 530°C for 10 hours to a thickness of 30 mm, and then hot
rolled at 390°C to a thickness of 4 mm. The sheets were
subsequently cold rolled to a thickness of 2 mm and then rapidly
annealed by heating rapidly to 480°C and holding at this
temperature for 5 minutes. Specimens prepared from the test
materials produced in the above process were evaluated by a
tensile test at a strain rate of 10-2/s at 480°C. Table 1 lists
the average crystal grain diameter for each specimen(as
measured at the sheet surface), the number per square
millimeter of grains of the AL-Fe-Si compound having a diameter
of 1 µm or above, and the elongation measurement results. Note
here that the grain count of the compound was made using image
processing.
As shown in Table 1, all of Materials No. 1 through 5
which comply with the present invention demonstrated
elongation exceeding 400%. On the other hand, both Material
No. 6 with an excessive Cu content, and Material No. 7 with
excessive Mg developed cracks during the hot rolling process
and failed to produce specimens. Further, Material No. 8 shows
inferior elongation due to the excessive amount of impurities
Fe and Si and the resultant number of large compound grains.
Finally, Material No. 9, containing insufficient amount of Mg,
also shows poor elongation due to lack of recrystallization
during the stretching deformation.
Al-Mg based aluminum alloys having compositions as
listed in Table 2 were melted and cast into ingots in the same
manner as in Examples 1, and made into 2-mm thick test materials
using the same process as in Examples 1. Specimens were then
evaluated in the same tensile test under the same conditions.
Table 2 lists the average crystal grain diameter, the number
per square millimeter of grains of the AL-Fe-Si compound having
a diameter of 1 µm or above, and the elongation measurement
results.
As shown in Table 2, all the Materials No. 10 through
12 which comply with the present invention demonstrated
elongation exceeding 380%. However, both Materials No. 13 and
No. 14, with their excessive Mn content, as well as Material
No. 15 with its excessive Cr content all showed inferior
elongation due to excessive distribution of the Al-Fe-Si
compound grains equal to or larger than 1 µm in diameter.
An aluminum alloy having the same composition as
Material No. 5 in Examples 1 was melted and cast in the same
manner as in the Examples 1, and the resultant ingot was
homogenized at 520°C for 8 hours to a thickness of 30 mm, then
hot-rolled starting at 390°C to a thickness of 4 mm. The sheet
was subsequently cold-rolled to a thickness of 2 mm and then
rapidly annealed by heating rapidly to 480°C and holding there
for 5 minutes. Specimens prepared from the test material
produced in the above process were evaluated in a tensile test
with varying strain rates and forming temperatures as
indicated in Table 3. The elongation measurement results are
as shown in Table 3. For guidance, the average crystal grain
diameter (as measured at the sheet surface) for all of these
specimens was in the range of 50 to 60 µm, and the number per
square millimeter of grains of the AL-Fe-Si compound having
a diameter of 1 µm or above, likewise, was below 2000.
| Material | Tensile Test Temperature (°C) | Strain Rate(/s) | Elongation (%) |
| 16 | 450 | 10-2 | 480 |
| 17 | 180 | 10-2 | 540 |
| 18 | 480 | 10-1 | 410 |
| 19 | 520 | 10-2 | 450 |
| 20 | 350 | 5 x 10-3 | 380 |
| 21 | 580 | 10-2 | 30 |
| 22 | 480 | 5 x 10-4 | 280 |
| 23 | 480 | 2 x 100 | 80 |
As shown in Table 3, all the Materials No. 16 through
19 which comply with the present invention demonstrated
elongation equal to or greater than 400%. However, the
Material No. 21 showed a diminished elongation result due to
its high tensile test temperature which resulted in coarse
crystal grains. The Materials No. 20 and No. 22, on the other
hand, showed poor elongation due to coarse crystal grains
formed during deformation because of too small a strain rate.
Finally, the Material No. 23 with too high a strain rate
employed also showed inferior elongation.
As described in the foregoing, the present invention
provides a method for the production of an Al-Mg aluminum alloy sheet having excellent
superplastic elongation in high speed forming such as at high
strain rate of 10-2 to 100/s at a high temperature, and a
superplastic forming process using this aluminum alloy sheet
shortens the forming time to improve productivity.
Claims (4)
- A method of producing an aluminum alloy sheet with excellent high-speed superplastic formability by melting an alloy comprising:3.0 to 8.0 wt. % Mg, 0.001 to 0.1 wt. % Ti, 0.06 wt. % or less of each Fe and Si, optionally 0.05 to 0.50 wt. % Cu, 0 to 50 ppm Be, not more than 0.10 wt. % Mn, not more than 0.1 wt. % Cr and the balance being Al and unavoidable impurities,casting and homogenising the alloy, followed by hot rolling at 250 to just under 400°C and annealing the alloy sheet at 350 to 550°C,and forming the so obtained alloy at a strain rate of 10-2 to 100/second at a temperature of 350 to 550°C with an elongation of more than 380 %.
- A method according to Claim 1 wherein the controlled amounts of Fe and Si are 0.05 or less.
- A method according to Claim 1 or Claim 2 wherein the number per square millimeter of grains of an Al-Fe-Si compound in the matrix structure of said alloy having a diameter of 1 µm or more is 2000 or less.
- A method according to Claims 1, 2 or 3 wherein the mean crystal grain diameter of an Al-Fe-Si compound is 25 - 200 µm.
Applications Claiming Priority (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP23770795A JP3145904B2 (en) | 1995-08-23 | 1995-08-23 | Aluminum alloy sheet excellent in high speed superplastic forming and its forming method |
| JP237707/95 | 1995-08-23 | ||
| JP23770795 | 1995-08-23 | ||
| PCT/JP1995/002564 WO1997008354A1 (en) | 1995-08-23 | 1995-12-12 | Aluminum alloy sheet excellent in high-speed superplastic formability and process of forming the same |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| EP0846781A1 EP0846781A1 (en) | 1998-06-10 |
| EP0846781A4 EP0846781A4 (en) | 1998-11-18 |
| EP0846781B1 true EP0846781B1 (en) | 2000-11-15 |
Family
ID=17019320
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| EP95940435A Expired - Lifetime EP0846781B1 (en) | 1995-08-23 | 1995-12-12 | Process of forming an aluminium sheet with excellent high speed superplastic formability |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20010001969A1 (en) |
| EP (1) | EP0846781B1 (en) |
| JP (1) | JP3145904B2 (en) |
| DE (1) | DE69519444T2 (en) |
| WO (1) | WO1997008354A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4534573B2 (en) * | 2004-04-23 | 2010-09-01 | 日本軽金属株式会社 | Al-Mg alloy plate excellent in high-temperature high-speed formability and manufacturing method thereof |
| EP1842935B1 (en) * | 2005-01-19 | 2014-10-29 | Kabushiki Kaisha Kobe Seiko Sho | Aluminum alloy plate and process for producing the same |
| WO2007080938A1 (en) | 2006-01-12 | 2007-07-19 | Furukawa-Sky Aluminum Corp. | Aluminum alloys for high-temperature and high-speed forming, processes for production thereof, and process for production of aluminum alloy forms |
| KR100676174B1 (en) * | 2006-05-25 | 2007-02-01 | 주식회사 엠코 | Attachment-free safety net support for steel construction frame |
| US8323428B2 (en) * | 2006-09-08 | 2012-12-04 | Honeywell International Inc. | High strain rate forming of dispersion strengthened aluminum alloys |
| JP2016191137A (en) * | 2015-03-31 | 2016-11-10 | 株式会社神戸製鋼所 | Aluminum alloy sheet for resin coated can body |
| JP2018199866A (en) * | 2018-08-24 | 2018-12-20 | 株式会社神戸製鋼所 | Aluminum alloy sheet for resin coated can body |
| CN113695538B (en) * | 2021-09-03 | 2023-07-25 | 中铝河南洛阳铝加工有限公司 | Preparation method of high-formability mirror aluminum plate strip and mirror aluminum plate strip |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS59159961A (en) * | 1983-02-28 | 1984-09-10 | Mitsubishi Alum Co Ltd | Superplastic al alloy |
| JPH02285046A (en) * | 1989-04-26 | 1990-11-22 | Sky Alum Co Ltd | Aluminum alloy rolled sheet for superplastic working and its manufacture |
| JP2517445B2 (en) * | 1990-06-05 | 1996-07-24 | スカイアルミニウム株式会社 | A1 alloy plate for forming diaphragm and method for manufacturing the same |
| JP2865499B2 (en) * | 1991-09-26 | 1999-03-08 | 健 増本 | Superplastic aluminum-based alloy material and method for producing superplastic alloy material |
| JP2510449B2 (en) * | 1992-01-31 | 1996-06-26 | スカイアルミニウム株式会社 | Method for manufacturing clad plate for roll bond panel |
| JPH05230583A (en) * | 1992-02-25 | 1993-09-07 | Mitsubishi Alum Co Ltd | High strength al alloy sheet excellent in formability |
| JPH05345963A (en) * | 1992-06-12 | 1993-12-27 | Furukawa Alum Co Ltd | Manufacture of high formability aluminum alloy sheet |
| DE69304009T2 (en) * | 1992-10-23 | 1997-02-06 | Kawasaki Steel Co | Process for the production of sheet metal from Al-Mg alloy for press molds |
| DE69303461T2 (en) * | 1992-11-17 | 1996-11-28 | Kawasaki Steel Co | Process for producing aluminum alloy sheet with excellent strength and deformability by deep drawing |
| JPH07145441A (en) * | 1993-01-27 | 1995-06-06 | Toyota Motor Corp | Superplastic aluminum alloy and its production |
| JPH06240395A (en) * | 1993-02-12 | 1994-08-30 | Sky Alum Co Ltd | Aluminum alloy sheet for superplastic forming, its production and superplastic formed body using it |
| JPH07197177A (en) * | 1994-01-10 | 1995-08-01 | Sky Alum Co Ltd | Aluminum alloy rolled sheet for superplastic formation and low in cavitation |
| JPH08199272A (en) * | 1995-01-19 | 1996-08-06 | Nippon Steel Corp | Aluminum alloy sheet and forming method |
-
1995
- 1995-08-23 JP JP23770795A patent/JP3145904B2/en not_active Expired - Fee Related
- 1995-12-12 DE DE69519444T patent/DE69519444T2/en not_active Expired - Fee Related
- 1995-12-12 US US09/000,097 patent/US20010001969A1/en not_active Abandoned
- 1995-12-12 WO PCT/JP1995/002564 patent/WO1997008354A1/en active IP Right Grant
- 1995-12-12 EP EP95940435A patent/EP0846781B1/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| WO1997008354A1 (en) | 1997-03-06 |
| EP0846781A4 (en) | 1998-11-18 |
| US20010001969A1 (en) | 2001-05-31 |
| EP0846781A1 (en) | 1998-06-10 |
| DE69519444D1 (en) | 2000-12-21 |
| JPH0959736A (en) | 1997-03-04 |
| DE69519444T2 (en) | 2001-06-13 |
| JP3145904B2 (en) | 2001-03-12 |
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