JPS6050141A - Hard aluminum alloy sheet for can end and its production - Google Patents

Abstract

PURPOSE:To produce a hard Al alloy sheet for a can end which permits reduction in thickness by subjecting an Al alloy casting ingot contg. a specific ratio of Mg and Cu to a specific treatment and specifying the average crystal grain size prior to final cold rolling. CONSTITUTION:An Al alloy casting ingot contg., by wt% 2.0-5.0% Mg and 0.05-0.50% Cu, contg. if necessary 0.05-0.50% Mn and 0.10-0.40% Cr and consisting of the balance substantially Al is subjected to soaking and hot rolling at 450-550 deg.C. The hot-rolled Al alloy is then heated to 400-600 deg.C at a heating rate of >=100 deg.C/min with or without cold rolling. The heated Al alloy sheet is cooled to <=200 deg.C at a cooling rate of >=100 deg.C/hr right after heating or after holding within 10min so that the average crystal grain size is made <=25mu and that the component incorporated therein to make contribution to prevention of conversion is made into a solid soln. state. The sheet is further subjected to the cold rolling at >=10% and the hard Al alloy sheet having an excellent bulging property, high strength and formability is obtd.

Description

DETAILED DESCRIPTION OF THE INVENTION The present invention relates to an aluminum plate for can ends, a hard alloy plate, and a method for manufacturing the same, and more specifically, the present invention relates to an aluminum plate for can ends, a hard alloy plate, and a method for manufacturing the same. Concerning the manufacturing method of the board.

In general, aluminum alloy plates for can ends are made by painting and printing on the aluminum alloy plate, and then (1) shell processing, (2) multi-stage overhang processing, (3) scoring, (4) reventing, and (5) seam j. 2I- The processing of the hat is done in 1j, but the most B in this addition 1.
The processing that is considered important is multi-stage elongation.
i HiX+'i +il'+ #: Affected by j diameter, etc.

In addition, the molded can end is required to have (1) pressure resistance, (2) readability,)) tough removal resistance, and (4) fillability. Nomu-1
(higher page strength) is required.

Increasing the strength and reducing the thickness of the material leads to a decrease in formability, and therefore, the thin wall 11- of the material has high IJ formability and high strength. However, the strength of conventionally used materials deteriorates dramatically during baking after coating and printing, so in order to achieve high strength, it is necessary to incorporate H elements (solid solution strengthening) and increase the final cold rolling rate. ”Nishō(
Lf, A + Shihito) are necessary. In the case of , -, the mechanical properties (elongation) are low and the crystal grain size ratio is low, resulting in low formability such as extensibility.

The strength of the present invention hardly decreases when the paint mark is 4:1llL%, and the strength is almost -1,
It is a bake-hard type, so it is possible to make the final cold rolling rate smaller than the current one. We present an aluminum alloy hard plate for can ends, which has particularly excellent elongation properties'(Nisu, 1:', +J strength and high formability, and has i+J ability to reduce the wall thickness), and a method for manufacturing the same.fJ1 There are .-4- things.

An aluminum alloy hard plate for can ends and its manufacturing method according to the present invention 1, 1, (1) + 2. (1-
5, (ltu1%, CuO, 05-0.50% containing 195%, balance'):, t'! Aluminum 1. The first invention is an aluminum alloy hard plate characterized by an average crystal grain size of 25 μm or more before cold open rolling. , (2) M+; 2,0...5. Axial 1%, CuO
,05-0,50u+t% 3i J waist Furthermore, M+1
0.05□-Q, 50u+t%, Cr (1,10=0
．． Contains 40u+t% and the rest? 1b (substantially white male) ＼1 is characterized by having a diameter of 25/I m or less, which is made of \1, and has a final cold-rolled + IJ uniform viscous product diameter of 25/I m or less. The aluminum alloy hard plate for the can end is the second invention and the waist (: () h1 shi, 2. +1 ~ 5
．． Ou+L%, C++ to 0.05, including 0.50 sail%, depending on the required crab, Mn (1,05 to 0.50t
llL%, Cr (1,10he (1,4 (1+u1%), the balance is naturally composed of ＼1 aluminum alloy ffJJ lump is soaked at a temperature of 450 to 550°C) Rolling, then cold rolling or no cold rolling, heating to a temperature of 400-600'C] at a heating rate of 00'C/min or less, immediately after heating or after holding for within 10 minutes, 1. oO'c/Hr] Yuno cooling rate c21
Cool to below 10°C to reduce the uniform grain size to 25μ or more.
・Ingredients that contribute to softening and softening are defined as hard iF(j), and then subjected to cold rolling of 10% or more. The present invention consists of three inventions, the first invention being an aluminum alloy hard plate for a can end.

The present invention [This aluminum alloy stone for can end XI]
! The quality plate and its manufacturing method will be explained in detail.

First, aluminum for the can end 1. 'N'& 4th flight 't￥ Root's content component J5 and component opening are explained in the first place.

N is an effective element for the strength direction of 1-, and 14+ has C, which is essential for obtaining the bake hard effect, and the content is only 2.01%. :l:i C' is 7(11), and 5.(1+++lJg
(at r-tυ'), is it possible to obtain high strength? However, the problem of lunar cracking of 1°1 occurs in the extension 11,1, and when the addition of 1. in the product is Therefore, jHf (1'jj', is 2.0-5
．． Let Ou+t%.

Cu is an element that has the same effect as H18, and the Bekehardt effect cannot be obtained at a content of 0.05u+t%::ei, and at a content of 0.5w1. If the content exceeds %, the expected effect will not be as good as that of its inclusion, but there may be problems in terms of scratch, corrosion, and corrosion resistance. Therefore, (9λ(i jil
, is (1,05-0,50 fields).

Although Mn cannot exceed the 1ti tangential effect for the bake-hard effect, the direction of strength is '-, the refinement of grains j;, 1 and the horn direction'.
It is effective in controlling l'1 (increasing the 45° direction ear),
This effect is small when the amount of 3f is less than 0.05u+t,%, and this effect is obtained when the content exceeds 0.50u+l%, but the intermetallic compound [A I6(M+++
This leads to the growth of the size of Fe) 1 grade, and becomes the starting point for the occurrence of cracking Jz, especially due to the multi-stage overhang processing of the 7F eel at the can end. Therefore, the Mn content is (1.05~0.50 1%
shall be.

Cr is an element effective in improving strength, and the content is 0.1
(If less than lu+t%, this effect is small, and 0.4
If the content exceeds 0+u1%, the size of the intermetallic compound will grow. Therefore, C' content is 0.
10-0.4 (lu+L%).

The elements contained in the pond are not particularly regulated as long as they are at the level of impurities C' normally contained in commercially available pure aluminum.

Next, the manufacturing method according to the present invention will be explained.

An aluminum alloy having the above-mentioned components and proportions is decasted by a normal method to form an ingot, and this ingot is soaked at 7:j degrees of 450 to 55 [)'C. However, this soaking treatment is to obtain suitable hot rolling and stretchability (especially small-diameter multi-step stretchability). If the heating temperature exceeds 55°C, edge cracking is likely to occur during hot rolling, and a large number of fine precipitates are formed, resulting in a decrease in elongation properties.
This leads to a decrease in product properties and surface quality. Therefore, the soaking crystallinity is set to 450 to 550'C.

In the subsequent hot rolling, there is no particularly restrictive strip 1'1,
It is preferable to finish hot rolling at a temperature of 250° C. or higher. Cold rolling may or may not be performed after this hot rolling.

Next is intermediate annealing, which is an important step in order to obtain a bake-hard effect and excellent properties (fine crystal grains) in formability, and the heating temperature is 4 () o -600°C. This is to form a solid solution of Mg and Cu, which are necessary for bake-hardening, and heating temperatures below 400°C do not sufficiently form a solid-solution, and the subsequent bake-hardening effect is not expected. At a heating temperature exceeding ℃, this effect is saturated and cannot be expected much, and instead causes burning etc., which leads to the characteristic 11(, l'. Therefore, the heating temperature is 40(1=[1(1(1 'C.

At this time, the heating rate was 100°C/m, and 100°C/l l r immediately after heating or after being held for less than 10 minutes.
It is essential to cool down to a temperature of 200°C or less at a cooling rate of
III.1.) and Mg and Cu are forcibly mixed into solid solution. Outside these ranges, the bake-hard effect and the high formability due to fine crystal grains cannot be achieved.

Note that holding the holding time within 10 minutes does not improve the bake-hard effect even if the holding time exceeds 10 minutes, and on the contrary causes crystal grain growth and wastes energy. The purpose of cooling to a temperature below C is to harden by baking.

Example 1 to explain an actual example of the aluminum alloy hard plate for can ends and the manufacturing method thereof according to the present invention An aluminum alloy ingot with the contents and components shown in Table 1 was subjected to soaking treatment of 500'CX old 1r. A 4 mm hot rolled plate was obtained by hot rolling. Thereafter, it was cold rolled to a thickness of 1 mm, and intermediate annealing was performed at 500'C'
・(.

The heating and cooling rates were set at 500'C/+n i n. Table 2 shows the grain size when this was cold rolled to a thickness of 0.30+ nm (geometrical properties (1,i: as rolled, after baking) and after intermediate annealing. rt,t'f
, is the 1'-average value determined by the cutting method.

From this Table 2, Rekaru, 1, sea urchin, present invention (No, l,
No, 2, No, 4 are AI Cu-Heshun type micro-i 11
The low strength 1ζ due to baking is smaller than that of the comparative example, and especially in the case of NO,,1, the tensile strength σ is in the opposite direction, and the crystal diameter η is smaller than that of the comparative example. All of them are 25 μm or less. As shown in Table 1 below, all moldability was good, but the present invention was superior in terms of high strength and high moldability. .

Example 2 When the intermediate annealing in Example 1 was carried out with: (Li (1'CX 2 peaks, heating and cooling rate of 40°C/Hr)
1,:tIIII+1'I (contract properties and V crystal 1'i IJ after intermediate annealing are shown in Table 3, and the formability is shown in Table 1.

From Tables 3 and 4, intermediate annealing is performed as shown in Table 3 and Table 4. When carried out at 1 (3 GO° (: , high strength is not achieved, and grain #J25/l after intermediate annealing
ml; Moon, roar, there is no problem in forming with the current plate thickness, but if the thickness is made thinner, a problem will occur.

Example 3 For alloy No. 1 shown in Table 1, intermediate annealing was performed by FSS.
Conducted under the conditions shown in the table, 0. :(1tlt when the decoy is 0 thick
Table 11 shows the mechanical properties and grains after open annealing. In addition, the 11 hours of holding at the reached temperature (heating temperature) is (lse
It is c.

As can be seen from Table 5, the heating temperature (achieved temperature) needs to be 4 (Xl'C or higher), and considering burning, etc., it is 400 to 60 (1'C heating?!a! If it is not a melon) Also, the heating rate is 100°C/Ill
If the cooling rate is less than i n, fine crystal grains cannot be obtained, and if the cooling rate is less than 100'C/Hr (1,7°C/+n1u), Cu and Mg, which are effective in baking bars, will precipitate during cooling, resulting in baking,... Nitrification during cleaning is not possible.

1. As explained above, the present invention includes A-, NJ
The manufacturing method for the aluminum alloy plate J, J, and Biku has the above-mentioned I'+Vi composition, so the bake-hard effect is utilized in the baking stage during coating printing. It maintains high strength, has excellent crystal grain shape, and is excellent in multi-cut extension IVI, which is the main forming process of 11+ conversion liquid Vents. It is something that plays.

Claims (3)

[Claims] (1) Mg 2.0-5.0IIIL%, Cu 000
5・-(1,5(lu+L%), the remainder is substantially A
1. An aluminum alloy hard plate for can ends, which is made of an aluminum alloy comprising: (2) Mg2.0-5. Ou+t%, CuO,05-
Contains 0.50u+L%, and further contains Mu 0.05-0.50ulL%, CrO, 10□
- An aluminum alloy containing (1,4(1+u1%) and the remainder substantially consisting of A1, and characterized in that the A/uniform grain size before the final cold rolling is 25 μm or less. End aluminum alloy hard plate. (3) M62.0-5. Ou+1%, Cu 0.05~
0.50+n1%, and optionally Mn 0.
05~0.5(l41%, 0'0.10~0.4(1w
An aluminum alloy ingot containing t% and the remainder substantially consisting of A1 is subjected to soaking and hot rolling at a temperature of 450 to 550°C, and then heated to 400 to 600°C with or without rolling. +00°C/m i
Heating at a heating rate of n or more, immediately after heating or holding within 10 minutes, and then cooling to 200°C or less at a cooling rate of 100°C/l+r or more -1- to reduce the average crystal grain size to 25μ or less. 1. A method for manufacturing aluminum and alloy hard plates for can ends, which comprises bringing the contained components contributing to prevention of softening into a solid solution state, and then subjecting them to cold rolling of 10% or more.