U.S. patent application number 10/553316 was filed with the patent office on 2007-03-22 for aluminum alloy plate excellent in press formability and continuous resistance spot weldability and method for production thereof.
This patent application is currently assigned to NIPPON LIGHT METAL COMPANY, LTD.. Invention is credited to Masaru Shinohara, Pizhi Zhao.
Application Number | 20070062618 10/553316 |
Document ID | / |
Family ID | 33302213 |
Filed Date | 2007-03-22 |
United States Patent
Application |
20070062618 |
Kind Code |
A1 |
Zhao; Pizhi ; et
al. |
March 22, 2007 |
Aluminum alloy plate excellent in press formability and continuous
resistance spot weldability and method for production thereof
Abstract
The invention offers an aluminum alloy plate with excellent
press-formability and continuous resistance spot weldability, and a
method of manufacturing such a plate. The aluminum alloy plate
comprises, in % by mass, 0.3-1.0% of Mg, 0.3-1.2% of Si, 0.10-1.0%
of Fe and 0.05-0.5% of Mn; where Fe+Mn.gtoreq.0.2%; the remainder
consisting of Al and unavoidable impurities; wherein an average
value of recrystallized grain size is 25 .mu.m or less; and at
least 5000 particles/mm.sup.2 of intermetallic compounds with a
circle-equivalent diameter of 1-6 .mu.m exist. It can further
contain 0.5-1.0% of Cu, 0.1-0.4% of Zr, 0.05% or less of Ti or
0.05% or less of Ti together with 0.01% or less of B. The invention
also offers a method of manufacturing an aluminum alloy plate
comprising steps of pouring a melt consisting of the above
composition into an opposing rotating belt caster that is forcibly
cooled; casting the melt at a cooling rate of 40-90.degree. C./sec
to form a 5-10 mm thick slab; drawing said slab from the side
opposite the side where the melt was poured; rolling directly or
after winding into a coil; and subjecting to a solution heat
treatment.
Inventors: |
Zhao; Pizhi; (Shizuoka,
JP) ; Shinohara; Masaru; (Shizuoka, JP) |
Correspondence
Address: |
MCKENNA LONG & ALDRIDGE LLP
1900 K STREET, NW
WASHINGTON
DC
20006
US
|
Assignee: |
NIPPON LIGHT METAL COMPANY,
LTD.
2-20, Higashi-Shinagawa 2-chome Shinagawa-ku
Tokyo
JP
1408628
|
Family ID: |
33302213 |
Appl. No.: |
10/553316 |
Filed: |
April 13, 2004 |
PCT Filed: |
April 13, 2004 |
PCT NO: |
PCT/JP04/05258 |
371 Date: |
October 23, 2006 |
Current U.S.
Class: |
148/551 ;
148/440; 420/546 |
Current CPC
Class: |
C22C 21/08 20130101;
B22D 11/124 20130101; C22F 1/043 20130101; B22D 11/003 20130101;
C22C 21/02 20130101; C22F 1/05 20130101; B22D 11/0605 20130101 |
Class at
Publication: |
148/551 ;
148/440; 420/546 |
International
Class: |
C22C 21/08 20060101
C22C021/08 |
Foreign Application Data
Date |
Code |
Application Number |
Apr 15, 2003 |
JP |
2003-110732 |
Feb 24, 2004 |
JP |
2004-048360 |
Claims
1. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability comprising, in % by mass,
0.3-1.0% of Mg, 0.3-1.2% of Si, 0.10-1.0% of Fe and 0.05-0.5% of
Mn; where Fe+Mn.gtoreq.0.2%; the remainder consisting of Al and
unavoidable impurities; wherein an average value of recrystallized
grain size is 25 .mu.m or less; and there are at least 5000
particles/mm.sup.2 of intermetallic compounds with a
circle-equivalent diameter of 1-6 .mu.m.
2. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 1,
further comprising 0.5-1.0% of Cu.
3. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 1,
further comprising 0.1-0.4% of Zr.
4. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 1,
further comprising 0.05% or less of Ti, or 0.05% or less of Ti and
0.01% or less of B.
5. A method of manufacturing an aluminum alloy plate with excellent
press-formability and continuous resistance spot weldability in
accordance with claim 1, comprising steps of pouring a melt
consisting of the above-claimed composition into an opposing
rotating belt caster that is forcibly cooled; casting the melt at a
cooling rate of 40-90.degree. C./sec to form a 5-10 mm thick slab;
drawing said slab from the side opposite the side where the melt
was poured; rolling directly or after winding into a coil; and
subjecting to a solution heat treatment.
6. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 2,
further comprising 0.1-0.4% of Zr.
7. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 2,
further comprising 0.05% or less of Ti, or 0.05% or less of Ti and
0.01% or less of B.
8. An aluminum alloy plate with excellent press-formability and
continuous resistance spot weldability in accordance with claim 3,
further comprising 0.05% or less of Ti, or 0.05% or less of Ti and
0.01% or less of B.
9. A method of manufacturing an aluminum alloy plate with excellent
press-formability and continuous resistance spot weldability in
accordance with claim 2, comprising steps of pouring a melt
consisting of the above-claimed composition into an opposing
rotating belt caster that is forcibly cooled; casting the melt at a
cooling rate of 40-90.degree. C./sec to form a 5-10 mm thick slab;
drawing said slab from the side opposite the side where the melt
was poured; rolling directly or after winding into a coil; and
subjecting to a solution heat treatment.
10. A method of manufacturing an aluminum alloy plate with
excellent press-formability and continuous resistance spot
weldability in accordance with claim 3, comprising steps of pouring
a melt consisting of the above-claimed composition into an opposing
rotating belt caster that is forcibly cooled; casting the melt at a
cooling rate of 40-90.degree. C./sec to form a 5-10 mm thick slab;
drawing said slab from the side opposite the side where the melt
was poured; rolling directly or after winding into a coil; and
subjecting to a solution heat treatment.
11. A method of manufacturing an aluminum alloy plate with
excellent press-formability and continuous resistance spot
weldability in accordance with claim 4, comprising steps of pouring
a melt consisting of the above-claimed composition into an opposing
rotating belt caster that is forcibly cooled; casting the melt at a
cooling rate of 40-90.degree. C./sec to form a 5-10 mm thick slab;
drawing said slab from the side opposite the side where the melt
was poured; rolling directly or after winding into a coil; and
subjecting to a solution heat treatment.
Description
TECHNICAL FIELD
[0001] The present invention relates to an aluminum alloy plate
with excellent press-formability and continuous resistance spot
weldability which is useful as a structural material for forming
the outer panels of products such as household appliances or
automobiles that are assembled by resistance spot welding before or
after press molding.
BACKGROUND ART
[0002] The structural materials and the outer panels of products of
household appliances and automobiles are pressed firstly forming,
then resistance spot welded to assemble the products.
[0003] Al--Mg--Si type alloy plates (JIS 6000) show a relatively
attractive surface appearance after press forming, and are
therefore used in various types of outer panels and structural
materials, but require good press-formability due to the diversity
of product shapes.
[0004] Additionally, there is a demand for increases in the number
of consecutive welds capable of being performed by resistance spot
welding in order to reduce the times the electrodes are replaced
during resistance spot welding work.
[0005] Japanese Patent Application, First Publication No.
S62-207851 describes a method for manufacturing a rolled plate such
as a body plate with good formability, comprising steps of
preparing an aluminum alloy melt containing 0.4-2.5% of Si,
0.1-1.2% of Mg, one or more types chosen from among 1.5% or less of
Cu, 2.5% or less of Zn, 0.3% or less of Cr, 0.6% or less of Mn and
0.3% or less of Zr, with the remainder consisting of Al and
unavoidable impurities; continuously casting the melt into 3-15 mm
thick slabs; performing cold rolling; and then performing a
solution heat treatment and quenching.
[0006] Additionally, Japanese Patent Application, First Publication
No. 2001-262264 describes Al--Mg--Si type aluminum alloy plates
used for automobile panels with good bendability. For example, the
publication discloses an Al--Mg--Si type aluminum alloy plate with
excellent toughness and bendability, basically comprising 0.1-2.0%
of Mg, 0.1-2.0% of Si and 0.1-1.5% of Fe in % by mass, with the
remainder consisting of Al, wherein the maximum size of Fe and Si
containing compounds is 5 .mu.m or less, and the average grain size
is 30 .mu.m or less. Additionally, it discloses an Al--Mg--Si type
aluminum alloy plate with excellent toughness and bendability,
basically comprising 0.1-2.0% of Mg, 0.1-2.0% of Si, 0.1-1.5% of Fe
and 2.0% or less of Fe in % by mass, with the remainder consisting
of Al, wherein the maximum size of Fe, Si and Cu containing
compounds is 5 .mu.m or less, and the average crystal grain size is
30 .mu.m or less. Furthermore, it discloses an Al--Mg--Si type
aluminum alloy plate with excellent toughness and bendability such
as those described above, further comprising at least one element
chosen from the group consisting of 1.0% or less of Mn, 0.3% or
less of Cr, 0.3% or less of Zr, 0.3% or less of V and 0.03% or less
of Ti.
[0007] The technique described in Japanese Patent Application,
First Publication No. S62-207851 uses a twin-roller casting process
with casting at a cooling rate of at least 100.degree. C./sec, so
that the size of intermetallic compounds that crystallize during
casting is small, as a result of which the number of relatively
large compounds that affect the grain size at recrystallization is
not sufficient, so that the grain size after solution heat
treatment is large, thus degrading the press-formability, and the
number of continuous resistance spot welds is reduced.
[0008] The technique disclosed in Japanese Patent Application,
First Publication No. 2001-262264 uses a continuous casting
process, with casting at a cooling rate of at least 10.degree.
C./sec, but in the examples, a maximum cooling rate of 30.degree.
C./sec is used. Due to the slow cooling rate, the size of
intermetallic compounds that crystallize during casting is large,
as a result of which the number of relatively large compounds that
affect the grain size at recrystallization is not sufficient, so
that the grain size after solution heat treatment is large, thus
degrading the press-formability and reducing the number of
continuous resistance spot welds.
DISCLOSURE OF THE INVENTION
[0009] The purpose of the present invention is to offer an aluminum
alloy plate with excellent press-formability and continuous
resistance spot weldability, and a manufacturing process
thereof.
[0010] The present inventors achieved the present invention on the
basis of the discovery that by selecting the optimum range for the
cooling rate when casting a melt within an appropriate composition
range, it is possible to optimize the size and number of
intermetallic compounds that crystallize, so as to obtain excellent
press-formability and continuous resistance spot weldability in an
aluminum alloy plate after a solution heat treatment.
[0011] That is, the present invention offers an aluminum alloy
plate with excellent press-formability and continuous resistance
spot weldability comprising, in % by mass, 0.3-1.0% of Mg, 0.3-1.2%
of Si, 0.10-1.0% of Fe and 0.05-0.5% of Mn; where
Fe+Mn.gtoreq.0.2%; the remainder consisting of Al and unavoidable
impurities; wherein an average value of recrystallized grain size
is 25 .mu.m or less; and there are at least 5000 particles/mm.sup.2
of intermetallic compounds with a circle-equivalent diameter of 1-6
.mu.m.
[0012] The present invention excels in press-formability and
continuous resistance spot weldability due to the fineness of the
recrystallization grain size and the large number of compounds of
optimum size.
[0013] The strength can be further improved by making the above
composition contain Cu in an amount of 0.5-1.0%.
[0014] The recrystallization grain size can be made finer and the
strength further improved by making the above composition contain
Zr in an amount of 0.1-0.4%.
[0015] Casting cracks can be reliably prevented from occurring
during casting by making the above composition contain Ti in an
amount of 0.05% or less, or Ti in an amount of 0.05% or less and B
in an amount of 0.01% or less.
[0016] A second aspect of the present invention is a method of
manufacturing an aluminum alloy plate with excellent
press-formability and continuous resistance spot weldability,
comprising steps of pouring a melt consisting of the above-claimed
composition into an opposing rotating belt cast that is forcibly
cooled; casting the melt at a cooling rate of 40-90.degree. C./sec
to form a 5-10 mm thick slab; drawing said slab from the side
opposite the side where the melt was poured; rolling directly or
after winding into a coil; and subjecting to a solution heat
treatment.
[0017] A large number of compounds of optimum size can be
crystallized by casting the alloy melt at an optimal cooling rate
when casting, thereby refining the recrystallization grain size to
result in aluminum alloy plates with excellent press-formability,
and continuous spot weldability is good.
BEST MODE FOR CARRYING OUT THE INVENTION
[0018] Herebelow, the preferable amounts of the respective
components contained in the aluminum alloy plates of the present
invention shall be described, followed by the reasons for the upper
and lower limits. In this specification, all quantities expressed
in % refer to percentage by mass except where indicated
otherwise.
[0019] [Mg: 0.3-1.0%]
[0020] [Si: 0.3-1.2%]
[0021] Mg and Si are added to improve the strength and to provide
press-formability. When the concentration is less than the
indicated lower limit, the effects are inadequate, and when more
than the indicated upper limit, the press-formability
deteriorates.
[0022] [Fe: 0.10-1.0%]
[0023] [Mn: 0.05-0.5%]
[0024] [Fe+Mn.gtoreq.0.2%]
[0025] By adding Fe and Mn together and keeping Fe+Mn.gtoreq.0.2%,
it is possible to crystallize a large quantity of compounds of a
specific size, increase the amount recrystallized, and the size of
the recrystallized grains becomes small. Both elements have little
effect when their concentration are less than the respective lower
limits, and when their concentrations exceed the upper limits,
cause bulky crystals to occur, so that surface blemishes such as
streaks can appear during cold rolling and the press-formability
also deteriorates. Mn does not crystallize into an intermetallic
compound of desirable size and number unless it coexists with Fe.
The total quantity of Fe and Mn is more preferably such that
Fe+Mn.gtoreq.0.3%.
[0026] [Cu: 0.5-1.0%]
[0027] Cu is added to further improve the strength and
press-formability. When the concentration is less than the lower
limit, its effect is small, and when the quantity exceeds the upper
limit, the corrosion resistance is degraded.
[0028] [Zr: 0.1-0.4%]
[0029] Zr promotes the crystallization of the intermetallic
compound Al.sub.3Zr, further induces crystallization of many
compounds of specific size to increase the number of recrystallized
nuclei, and thereby make the size of the recrystallized grains
smaller, so as to improve press-formability. The effect is lost
when the concentration is less than the lower limit, and when the
quantity exceeds the upper limit, large compounds are formed so
that the rollability is reduced.
[0030] [Ti: 0.05% or less; or Ti: 0.05% or less and B: 0.01% or
less]
[0031] Rapid cooling during casting of the melt can cause casting
cracks to occur, and the addition of Ti or Ti and B can prevent
such cracks. It is possible to add either Ti alone at a quantity of
0.05% or less, or to also add 0.01% or less of B to obtain a
composite with Ti, in which case there is a synergistic effect. The
effect is most apparent when the lower limit of the Ti is at least
0.002%, and the lower limit of B is at least 0.0005%.
[0032] The unavoidable impurities can come from the base aluminum,
scrap and ingot jigs or the like, some of the typical elements
including Cr, Ni, Zn, Ga and V. Since Cr is added to prevent stress
corrosion of the Al--Mg alloy, it can easily be introduced from
scrap, but is allowable in the present invention if less than 0.3%.
The quantity of Ni should be held to less than 0.2%, that of Ga and
V respectively less than 0.1%, and that of any other unavoidable
impurities to less than 0.3% in order to maintain the
formability.
[0033] [Average Recrystallization Grain Size 25 .mu.m or Less]
[0034] If the recrystallized grains of plates after the solution
heat treatment are small, then they can be formed without damage
even if the press draft is set high and the drawing height is set
high. If the grains size exceeds the upper limit, the effect is
lost, and the surface appearance after pressing is not good. The
recrystallization grain size should preferably be 20 .mu.m or less,
and 15 .mu.m or less.
[0035] [5000/mm.sup.2 Intermetallic Compounds with Circle
Equivalent Diameter of 1-6 .mu.m]
[0036] Intermetallic compounds having a circle equivalent diameter
of 1-6 .mu.m are of a size promoting the accumulation the
integration of dislocations during cold rolling and having an
effect of refining the recrystallized grains, so that if the size
and number is less than the lower limit, the dislocation
accumulation rate is low, and if the number is less than 5000
particles/mm.sup.2, fine recrystallized grains of a preferable size
cannot be obtained. Additionally, if the size exceeds the upper
limit, the large compounds can cause streaks or cracks during
rolling and thereby lower the rollability. Additionally, with the
state of the compounds as described above, a erosion effect
occurring due to a reaction between the copper electrodes and the
Al when performing continuous resistance spot welding can be
prevented, thus reducing the number of times the electrode needs to
be replaced and improving the productivity. The quantity of the
compounds is more preferably at least 6000 particles/mm.sup.2
[0037] Next, a preferable process for manufacturing the aluminum
alloy plates of the present invention shall be described.
[0038] The melt is prepared by adjusting the composition,
degassing, settling, making fine adjustments of the composition as
needed, adding Ti or Ti and B as a mother alloy and casting. When
casting, the melt is poured into forcibly cooled rotating belters
facing each other, with the cooling rate 40-90.degree. C./sec, to
form a 5-10 mm thick slab, then drawing the slab from the opposite
side to where the melt was poured, to roll it directly or after
winding into a coil.
[0039] Continuous casting processes include a twin-roller casting
process of pouring the melt between forcibly cooled rotating
rollers that are facing each other, rapidly cooling the melt on the
roller surfaces, and continuously withdrawing thin slabs from the
opposite side, and a twin-belt casting process of pouring the melt
between forcibly cooled rotating belts that are facing each other,
rapidly cooling the melt on the belt surfaces, and continuously
withdrawing thin slabs from the opposite side.
[0040] The twin-roller casting process has a cooling rate during
casting of at least 300.degree. C./sec which is considerably high,
while the size of compounds in the resulting slab are small and the
plates of the present invention are not obtained. On the other
hand, the twin-belt casting process involves rapidly cooling the
melt on the belt surface, but the cooling rate is not as high as
with the twin-roller casting process.
[0041] In the present invention, the casting conditions of the
twin-belt casting process are adjusted so as to make the melt
cooling rate 40-90.degree. C./sec (at a position of 1/4 thickness
of the slab), so as to form more than 5000 particles/mm.sup.2 of
intermetallic compounds with a circle-equivalent diameter of 1-6
.mu.m in the final plates. If the melt cooling rate is less than
40.degree. C./sec, larger compounds are crystallized, causing a
deficiency of compounds in the above-defined size range, so that
the recrystallized grains are not refined and plates with excellent
press-formability cannot be obtained. Additionally, at more than
90.degree. C./sec, fine compounds are crystallized, causing a
reduction of compounds in the above-defined size range, so that a
plate with refined recrystallized grains cannot be obtained.
[0042] A slab obtained by a twin-belt casting process is
cold-rolled to form a plate of a desired thickness, which undergoes
a solution heat treatment and is recrystallized. At this time, it
is possible to provide an anneal during the cold rolling step, but
the rolled plate provided for the solution heat treatment has at
least a cold reduction of 55%. The solution heat treatment is
performed in a continuous annealing furnace. The heating
temperature is at least 500.degree. C., the cooling rate to
100.degree. C. is set to at least 1.degree. C./sec. The
recrystallized grains of the rolled plates that have undergone the
solution heat treatment have an average grain size of 25 .mu.m or
less due to the size and number of the intermetallic compound and
the reduction. Such plates can be used either as they are, or after
passing through a skin pass or leveler of about 1-5% in order to
obtain flatness.
EXAMPLES
[0043] An aluminum alloy melt with the composition shown in Table 1
was degassed, settled, then the melt was cast into a 7 mm thick
slab at cooling rates of 50.degree. C./sec and 75.degree. C./sec in
a twin-belt continuous casting process. The slab drawing speed was
8 m/min. This slab was cold-rolled, and subjected to an
intermediate annealing treatment as needed to form a 1 mm thick
plate. Next, this plate was subjected to a solution heat treatment,
and after the treatment, the size and number of intermetallic
compounds, recrystallization grain size, 0.2% yield strength (YS),
ultimate tensile strength (UTS), elongation (EL), deep drawing
height and resistance spot weldability were measured. The results
are shown in Table 3.
[0044] The deep drawing conditions and evaluation conditions for
the resistance spot weldability were as shown below.
[0045] (Deep Drawing Test) TABLE-US-00001 Mold Used Punch diameter
50 mm shoulder R 5 mm Dies inner diameter 52.5 mm shoulder R 8 mm
Blank diameter 112.5 mm (Evaluation Conditions for Resistance Spot
Weldability) Single Phase Rectifier Type Spot Welding Machine
Electrode Cu--1%Cr Alloy Pressure 400 kgf
Determination of Welding Current: Minimum welding current where
tensile shear strength satisfies grade A average standard as
defined by JIS Z3140. Consecutive welding spots: Number of welding
consecutively with strength exceeding grade A average standard when
continuous spot welding using the welding current values determined
above and with the above welding conditions.
[0046] A: at least 500 consecutive hits
[0047] B: at least 200 less than 500 consecutive hits
[0048] C: less than 200 consecutive hits TABLE-US-00002 TABLE 1
Alloy Composition (units in % by mass) Alloy No. Mg Si Fe Mn Cu Zr
Ti B Comments A 0.6 0.8 0.12 0.1 -- -- 0.02 Present Invention B 0.4
0.8 0.2 0.2 -- -- 0.02 Present Invention C 0.5 0.7 0.2 0.2 -- --
0.02 Present Invention D 0.5 0.8 0.2 0.2 -- -- 0.01 Present
Invention E 0.6 0.8 0.7 0.1 -- -- 0.02 Present Invention F 0.5 0.9
0.15 0.3 -- -- 0.02 Present Invention G 0.5 0.7 0.2 0.2 0.6 -- 0.02
Present Invention H 0.5 0.7 0.2 0.2 -- 0.15 0.02 Present Invention
I 0.5 0.7 0.2 0.2 0.7 0.12 0.02 Present Invention J 1.2 0.7 0.2 0.2
-- -- 0.02 Comparative Example K 0.5 1.4 0.2 0.2 -- -- 0.02
Comparative Example L 0.5 0.7 0.05 0.2 -- -- 0.02 Comparative
Example M 0.5 0.7 1.5 0.2 -- -- 0.02 Comparative Example N 0.5 0.7
0.2 0.7 -- -- 0.02 Comparative Example O 0.5 0.7 0.2 0.2 1.2 --
0.02 Comparative Example P 0.5 0.7 0.2 0.2 -- 0.5 0.02 Comparative
Example (Note) Remainder: Al and impurities. Underlined values are
outside the range of the present invention.
[0049] TABLE-US-00003 TABLE 2 Manufacturing Process Alloy Cast
Methods/ Cooling Rate Hot Roll Cold Roll Interm. Anneal Temp Cold
Roll Soln. Heat Tr. No. No. Slab Thickness (mm) (.degree. C./sec)
(mm) (mm) (.degree. C.)/hour (h) (mm) Temp. (.degree. C.) Comm. 1 A
twin belt/7 50 -- -- -- 1 550.degree. C. Pres Inv 2 B twin belt/7
50 -- -- -- 1 550.degree. C. Pres Inv 3 C twin belt/7 50 -- -- -- 1
550.degree. C. Pres Inv 4 D twin belt/7 50 -- -- -- 1 550.degree.
C. Pres Inv 5 E twin belt/7 50 -- -- -- 1 550.degree. C. Pres Inv 6
F twin belt/7 50 -- -- -- 1 550.degree. C. Pres Inv 7 G twin belt/7
50 -- -- -- 1 550.degree. C. Pres Inv 8 H twin belt/7 50 -- -- -- 1
550.degree. C. Pres Inv 9 I twin belt/7 50 -- -- -- 1 550.degree.
C. Pres Inv 10 C twin belt/7 50 -- 2.5 360/2 1 550.degree. C. Pres
Inv 11 B twin belt/7 75 -- -- -- 1 550.degree. C. Pres Inv 12 J
twin belt/7 50 -- -- -- 1 550.degree. C. Comp Ex 13 K twin belt/7
50 -- -- -- 1 550.degree. C. Comp Ex 14 L twin belt/7 50 -- -- -- 1
550.degree. C. Comp Ex 15 M twin belt/7 50 -- -- -- 1 550.degree.
C. Comp Ex 16 N twin belt/7 50 -- -- -- 1 550.degree. C. Comp Ex 17
O twin belt/7 50 -- -- -- 1 550.degree. C. Comp Ex 18 P twin belt/7
50 -- -- -- 1 550.degree. C. Comp Ex 19 B twin belt/20 20 3 -- -- 1
550.degree. C. Comp Ex 20 B twin belt/3 150 -- -- -- 1 550.degree.
C. Comp Ex (Note) Underlined values are outside the range of the
present invention.
[0050] TABLE-US-00004 TABLE 3 Microstractures and Properties
Density of Intermetallic Grain size Tensile Properties Deeping
Drawing Resistance Spot No. Compound (/mm.sup.2) (.mu.m) 0/2% YS
(MPa) UTS (MPa) EL (%) Height(mm) Weldability Comments 1 5917 12
130 238 28 14.5 B Present Invention 2 6812 11 118 222 29 14.1 A
Present Invention 3 7185 10 124 228 28 14.3 A Present Invention 4
7726 9 132 239 30 14.7 A Present Invention 5 11254 7 145 249 27
14.2 A Present Invention 6 6917 11 128 235 29 14.8 A Present
Invention 7 7435 10 135 264 29 14.9 A Present Invention 8 7982 8
126 230 29 14.8 A Present Invention 9 8013 8 137 266 30 14.9 A
Present Invention 10 6725 15 114 219 27 14.0 A Present Invention 11
7820 9 122 230 30 15.1 A Present Invention 12 7543 11 140 252 24
13.5 A Comp. Example 13 7521 9 131 251 23 13.6 A Comp. Example 14
3924 26 112 215 26 13.5 C Comp. Example 15 36721 6 133 241 21 13.5
A Comp. Example 16 7820 11 134 248 20 13.7 A Comp. Example 17 7541
9 160 288 22 13.8 A Comp. Example 18 8783 7 142 235 21 13.9 A Comp.
Example 19 2215 29 109 215 20 12.5 C Comp. Example 20 3272 26 113
218 22 12.8 C Comp. Example (Note) A: at least 500 consecutive hits
B: at least 200 less than 500 consecutive hits C: less than 200
consecutive hits Underlined values are outside the range of the
present invention. Recrystallized grain size was measured by liner
intercept method.
From the results in Tables 1-3, it is apparent that the examples of
the present invention (Sample Nos. 1-11) have a high deep drawing
height and excel in press-formability, as well as having many
consecutive hits and excelling in continuous resistance spot
weldability. On the other hand, the comparative examples (Samples
Nos. 12-18) whose compositions are outside the range of the present
invention have a low deep drawing height and poor
press-formability, while the comparative examples (Samples Nos. 14,
19, 20) with few intermetallic compounds with a circle-equivalent
diameter of 1-6 .mu.M and a large grain size had few consecutive
hits and poor continuous resistance spot weldability.
[0051] As described above, the aluminum alloy plates according to
the present invention excel in press-formability and continuous
resistance spot weldability, and surface appearance after press is
good, enabling continuous assembly by resistance spot welding,
therefore productivity is high. This 6000 type alloy plate also has
higher strength improves in a baking step after coating or the
like, so as to have excellent industrial value in a wide range of
applications such as in the body panels of automobiles.
* * * * *