JPH028353A - Manufacture of aluminum alloy for forming excellent in baking strength - Google Patents
Manufacture of aluminum alloy for forming excellent in baking strengthInfo
- Publication number
- JPH028353A JPH028353A JP16035988A JP16035988A JPH028353A JP H028353 A JPH028353 A JP H028353A JP 16035988 A JP16035988 A JP 16035988A JP 16035988 A JP16035988 A JP 16035988A JP H028353 A JPH028353 A JP H028353A
- Authority
- JP
- Japan
- Prior art keywords
- strength
- baking
- alloy
- ingot
- aluminum alloy
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 20
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 8
- 238000010438 heat treatment Methods 0.000 claims abstract description 18
- 238000001816 cooling Methods 0.000 claims abstract description 16
- 239000013078 crystal Substances 0.000 claims abstract description 10
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 229910052796 boron Inorganic materials 0.000 claims abstract description 6
- 238000005098 hot rolling Methods 0.000 claims abstract description 6
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 238000005482 strain hardening Methods 0.000 claims description 5
- 229910045601 alloy Inorganic materials 0.000 claims description 4
- 239000000956 alloy Substances 0.000 claims description 4
- 238000000265 homogenisation Methods 0.000 claims description 4
- 238000000465 moulding Methods 0.000 claims description 4
- 238000005097 cold rolling Methods 0.000 abstract description 6
- 239000000203 mixture Substances 0.000 abstract description 6
- 238000000034 method Methods 0.000 abstract description 3
- 238000010422 painting Methods 0.000 abstract description 3
- 230000001105 regulatory effect Effects 0.000 abstract description 3
- 229910052725 zinc Inorganic materials 0.000 abstract description 3
- 229910052748 manganese Inorganic materials 0.000 abstract description 2
- 230000000694 effects Effects 0.000 description 15
- 239000000243 solution Substances 0.000 description 8
- 230000000052 comparative effect Effects 0.000 description 7
- 239000000463 material Substances 0.000 description 7
- 239000000126 substance Substances 0.000 description 6
- 229910052749 magnesium Inorganic materials 0.000 description 5
- 239000000047 product Substances 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000007796 conventional method Methods 0.000 description 3
- 229920006395 saturated elastomer Polymers 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 238000009776 industrial production Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 238000005096 rolling process Methods 0.000 description 2
- 229910016570 AlCu Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 230000000996 additive effect Effects 0.000 description 1
- 229910052782 aluminium Inorganic materials 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 239000010419 fine particle Substances 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- 230000007774 longterm Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
Landscapes
- Metal Rolling (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明は、成形加工用アルミニウム合金の製造に係り、
より詳細には、特に自動車、車両等、車体加工用として
成形加工性が良好で、特に塗装後のベーキング強度が非
常に優れたアルミニウム合金の製造方法に関するもので
ある。DETAILED DESCRIPTION OF THE INVENTION (Field of Industrial Application) The present invention relates to the production of an aluminum alloy for forming,
More specifically, the present invention relates to a method for producing an aluminum alloy that has good moldability for processing car bodies, such as automobiles and vehicles, and has particularly excellent baking strength after painting.
（従来の技術及び解決しようとする課題）最近、自動車
、車両用材料には、機能の多様化及び高度化による重量
増加に伴い、燃費の向上、操縦性の向上等々のために軽
量化を図るべく、鋼材料に代ってアルミニウム合金板が
使用され始めてきている。(Conventional technology and issues to be solved) Recently, as the weight of automobiles and vehicle materials has increased due to diversification and sophistication of functions, efforts have been made to reduce the weight of automobiles and vehicle materials in order to improve fuel efficiency, improve maneuverability, etc. Therefore, aluminum alloy plates are beginning to be used instead of steel materials.
このような用途に使用されるアルミニウム合金板におい
ては、成形加工性が重要であり、低耐力で形状凍結性が
良く、しかも耐プント性等の向上のために成形加工→塗
装後の焼付工程（ベーキング）において強度が高くなる
ことが要求されている。For aluminum alloy sheets used in such applications, formability is important, and in order to have low yield strength and good shape fixability, and to improve Punto resistance, etc., the process of forming → baking after painting ( It is required to have high strength in baking).
ところが、従来、車両用等に用いられているアルミニウ
ム合金のうち、Ａｆｌ−Ｍｇ系のアルミニラム合金とし
て５０５２．５１５４．５０８６．５１８２．５０８３
合金等があるが、いずれも成形加工性、耐食性等は優れ
ていても、成形加工後のベーキング強度が低いという欠
点があった。このため、強度を確保するには板厚を厚く
せざるを得す、軽量化効果が小さいことが問題であった
。However, among the aluminum alloys conventionally used for vehicles, 5052.5154.5086.5182.5083 is an Afl-Mg-based aluminum alloy.
There are alloys, etc., but although they all have excellent moldability, corrosion resistance, etc., they have the drawback of low baking strength after molding. For this reason, the problem was that the plate thickness had to be increased to ensure strength, and the weight reduction effect was small.
一方、ベーキング強度を高くするために、ＡｌＣｕ系の
２０３６やＡｌ−Ｍｇ−３ｉ系の６００９．６０１０合
金等が使用されているが、成形加工性が劣ったり、或い
は強度が不十分であったり、更には材料製造後の経時変
化により強度が高くなり、プレス加工時に形状凍結性が
悪くなったりするという問題があった。On the other hand, in order to increase baking strength, AlCu-based 2036 and Al-Mg-3i-based 6009.6010 alloys are used, but they have poor moldability or insufficient strength. Furthermore, there was a problem in that the strength increased due to changes over time after the material was manufactured, and shape fixability deteriorated during press working.
本発明は、上記従来技術の問題点を解決するためになさ
れたものであって、従来材の５０５２．５１８２等と同
等以上の成形性を有し、しかもベーキング後の強度が極
めて高い成形加工用アルミニウム合金の製造方法を提供
することを目的とするものである。The present invention has been made in order to solve the problems of the prior art described above, and has moldability equivalent to or better than conventional materials such as 5052.5182, and has extremely high strength after baking. The object of the present invention is to provide a method for producing an aluminum alloy.
（課題を解決するための手段）
か＼る目的を達成するため、本発明者らは、従来材に上
記の如く問題があることに鑑みて、その対策を見い出す
べく鋭意研究を行った。(Means for Solving the Problem) In order to achieve the above object, the inventors of the present invention, in view of the above-mentioned problems with conventional materials, conducted intensive research to find a countermeasure.
その結果、所定量のＭｇ、Ｚｎ及びＣｕを必須成分とし
、これに適量のＭｎ、Ｃｒ、Ｔｉ及びＢの少なくとも１
種以上を添加して化学成分を調整すると共に、鋳塊の結
晶粒度、最終冷延加工率及び最終板厚での熱処理条件、
すなわち、溶体化処理条件、冷却条件等を規制すること
により、可能であることを見い出し、ここに本発明をな
したものである。As a result, predetermined amounts of Mg, Zn, and Cu are essential components, and appropriate amounts of at least one of Mn, Cr, Ti, and B are added.
In addition to adjusting the chemical composition by adding seeds or more, the grain size of the ingot, the final cold rolling rate, the heat treatment conditions at the final plate thickness,
That is, we have discovered that it is possible by regulating the solution treatment conditions, cooling conditions, etc., and have hereby accomplished the present invention.
すなわち、本発明に係るベーキング強度に優れた成形加
工用アルミニウム合金の製造方法は、Ｍｇ：３．Ｏ−５
，０％、Ｚｎ：０．０Ｂ−０，６％及びＣｕ：０．３〜
２．０％を必須成分とし、更にＭｎ：０゜０３〜０．５
％、Ｃｒ：０．０３〜０．３％、Ｔｉ： ０ 。That is, the method for producing an aluminum alloy for forming with excellent baking strength according to the present invention is as follows: Mg: 3. O-5
, 0%, Zn: 0.0B-0.6% and Cu: 0.3~
2.0% is an essential component, and Mn: 0゜03~0.5
%, Cr: 0.03-0.3%, Ti: 0.
００５〜０．３％及びＢ：Ｏ，ＯＯＯ５〜０．０５％の
うちの１種又は２種以上を含有し、残部がＡ Ｄ。005-0.3% and B:O, OOO5-0.05%, and the remainder is AD.
及び不可避的不純物からなるＡｆ１合金につき、結晶粒
径が１．５ｍｍ以下の鋳塊を用い、均質化処理後、熱間
圧延を行い、次いて最終の冷間加工率を６０％以上与え
て所定の板厚とし、引き続いて、１００°Ｃ／ｍｉｎ以
上の加熱速度で４５０−５６０”ＣＸ １００秒以下の
加熱を行った後、冷却速度２００℃／ｍｉｎ以上で冷却
することを特徴とするものである。For the Af1 alloy, which contains unavoidable impurities, an ingot with a crystal grain size of 1.5 mm or less is used, and after homogenization treatment, hot rolling is performed, and then a final cold working rate of 60% or more is applied to the specified rolling process. It is characterized by having a thickness of 450-560" CX for 100 seconds or less at a heating rate of 100°C/min or more, and then cooling at a cooling rate of 200°C/min or more. be.
以下に本発明を更に詳細に説明する。The present invention will be explained in more detail below.
（作用） まず、本発明における化学成分の限定理由を述べる。(effect) First, the reason for limiting the chemical components in the present invention will be described.
Ｍｇ：
Ｍｇは、ベーキング性、強度、成形加工性の向上に寄与
する元素である。しかし、３．０％未満ではベーキング
性が悪く、強度が低い。また５゜０％を超えると強度は
高くなるが、圧延時に割れが起こり易くなり、通常の工
業的製造が困難になる。したがって、Ｍｇ量は３．０〜
５．０％の範囲とする。Mg: Mg is an element that contributes to improving baking properties, strength, and moldability. However, if it is less than 3.0%, baking properties are poor and strength is low. If it exceeds 5.0%, the strength will be high, but cracks will easily occur during rolling, making normal industrial production difficult. Therefore, the Mg amount is 3.0~
The range shall be 5.0%.
Ｃｕ：
Ｃｕは、Ｍｇと同様、ベーキング性、強度、成形加工性
の向上に寄与する元素であり、特にＭｇと共存するとそ
の効果は一層大きくなる。しかし、０．３％未満ではベ
ーキング後の強度が低く、また２、０％を超えるとベー
キング強度は飽和してしまい、通常の工業的製造が難し
くなる。したがって、Ｃｕ量は０．３〜２．０％の範囲
とする。Cu: Similar to Mg, Cu is an element that contributes to improving baking properties, strength, and moldability, and its effects are particularly enhanced when it coexists with Mg. However, if it is less than 0.3%, the strength after baking will be low, and if it exceeds 2.0%, the baking strength will be saturated, making normal industrial production difficult. Therefore, the amount of Cu is in the range of 0.3 to 2.0%.
Ｚｎ：
Ｚｎは成形加工性、ベーキング性の向上に寄与する元素
であるが、０．０６％未満ではその効果はなく、また０
、６％を超えて添加してもその効果は飽和し、むしろ耐
食性が著しく悪くなり、使用できなくなる。したがって
、Ｚｎ量は０．０６〜０．６％の範囲とする。Zn: Zn is an element that contributes to improving moldability and baking properties, but if it is less than 0.06%, it has no effect and
, even if it is added in excess of 6%, the effect is saturated and the corrosion resistance deteriorates significantly, making it unusable. Therefore, the amount of Zn is set in the range of 0.06 to 0.6%.
以上の各元素を必須成分とするが、以下に示す元素のＭ
ｎ、Ｃｒ、Ｔｉ及びＢのうちの１種又は２種以上を含有
させる必要がある。Each of the above elements is an essential component, but the M of the elements shown below is
It is necessary to contain one or more of n, Cr, Ti, and B.
Ｍｎ：
Ｍｎは成形加工性と強度の向上に寄与する元素であるが
、０．０３％未満ではその効果がなく、また０、５％を
超えると成形加工性が劣るので、好ましくない。このた
め、Ｍｎ量は０．０３〜０゜５％の範囲とする。Mn: Mn is an element that contributes to improving moldability and strength, but if it is less than 0.03%, it has no effect, and if it exceeds 0.5%, moldability is poor, so it is not preferable. Therefore, the amount of Mn is set in the range of 0.03 to 0.5%.
Ｃｒ：
Ｃｒは強度と成形加工性の向上に寄与する元素であるが
、０．０３％未満てはその効果が少なく、また０、３％
を超えて添カ１比でも強度の改善効果が飽和し、むしろ
成形加工性が劣るので、好ましくない。このため、Ｃｒ
量は０．０３〜０．３％の範囲とする。Cr: Cr is an element that contributes to improving strength and formability, but less than 0.03% has little effect, and 0.3%
Even if the additive ratio exceeds 1, the strength improvement effect is saturated, and the moldability is rather poor, which is not preferable. For this reason, Cr
The amount should be in the range of 0.03-0.3%.
Ｔ１、Ｂ：
Ｔ１とＢは結晶粒微細化による成形加工性、強度の向上
に寄与する元素であるが、それぞれＴｉＯ，００５％未
満、ＢＯ，０Ｏ０５％未ａではソノ効果がなく、またＴ
１が０．３％超、Ｂが。、０５％超では伸びが低下し、
成形加工性が劣るので、好ましくない。したがって、Ｔ
ｉ量は０．００５〜０．３％、Ｂ量は０．０００５−０
．０５％の範囲とする。T1, B: T1 and B are elements that contribute to improving formability and strength through grain refinement, but if TiO is less than 0.05% and BO is less than 0.05%, there is no sono effect, and T
1 exceeds 0.3%, B. , the elongation decreases when it exceeds 0.05%,
It is not preferred because the molding processability is poor. Therefore, T
The amount of i is 0.005-0.3%, the amount of B is 0.0005-0
．． The range is 0.05%.
なお、」１記化学成分のアルミニウム合金には不純物が
含まれるが、不純物量は可及的に少ないのが好ましく、
例えば、Ｆｅ、Ｓｉはそれぞれ０．５％以下、■、Ｎｉ
等その他の元素は０．１％以下であれば、本発明の効果
を損なうものではない。In addition, although the aluminum alloy of chemical composition 1 contains impurities, it is preferable that the amount of impurities be as small as possible.
For example, Fe and Si are each 0.5% or less, ■, Ni
If the content of other elements is 0.1% or less, the effects of the present invention will not be impaired.
次に本発明の製造プロセスの条件について説明する。Next, the conditions of the manufacturing process of the present invention will be explained.
まず、上記化学成分を有するアルミニウム合金は常法に
より溶製し、鋳造して鋳塊を得る。First, an aluminum alloy having the above chemical components is melted by a conventional method and cast to obtain an ingot.
但し、鋳塊の結晶粒径は、製品の結晶粒微細化に大きく
影響を及ぼすので、１．５ｍｍ以下とする必要がある。However, since the crystal grain size of the ingot has a large effect on the grain refinement of the product, it needs to be 1.5 mm or less.
これは、上記組成のＡｌ合金鎚塊を均質化処理し、熱間
圧延、冷間圧延をして所定の板厚にした時に、鋳塊の結
晶粒径が１． 、５ ｍｍを超えるものではその後の工
程によっても、製品の結晶粒微細化効果が少なく、成形
加工性、ベーキング強度等が悪くなるためである。This means that when an Al alloy hammered ingot with the above composition is homogenized, hot-rolled and cold-rolled to a predetermined thickness, the crystal grain size of the ingot is 1. This is because if the diameter exceeds 5 mm, subsequent steps will have little effect on refining the crystal grains of the product, resulting in poor moldability, baking strength, etc.
この鋳塊に対する均質化処理、熱間圧延までは通常の方
法を用いればよい。例えば、上記鋳塊を必要に応じて４
５０〜５５０℃で１〜４８時間加熱保持する均質化処理
を行い、常法に従って熱間圧延を行う。なお、その後、
必要に応して荒焼鈍（例、３５０〜ｂ
もよい。Conventional methods may be used for the homogenization treatment and hot rolling of this ingot. For example, if necessary, the above ingot is
Homogenization treatment is performed by heating and holding at 50 to 550°C for 1 to 48 hours, and hot rolling is performed according to a conventional method. Furthermore, after that,
Rough annealing (for example, 350-b may also be used if necessary).
次いで、冷間圧延を行う。但し、冷間圧延は最終の冷間
加工率６０％以上で圧延し、所定の板厚とする必要があ
る。冷間加工率が６０％未満ではその後の熱処理により
固溶化促進が行われず、成形加工後のベーキング工程に
おいて強度向上を図ることができず、好ましくない。Next, cold rolling is performed. However, the cold rolling must be performed at a final cold working rate of 60% or more to obtain a predetermined plate thickness. If the cold working ratio is less than 60%, the subsequent heat treatment will not promote solid solution formation, making it impossible to improve the strength in the baking step after forming, which is not preferable.
次に、最終熱処理として、１００℃／ｍｉｎ以上の加熱
速度で４５０〜ｂ
温度範囲、時間範囲で溶体化処理し、２００℃／ｍｉｎ
以上の冷却速度で冷却する。Next, as a final heat treatment, solution treatment is performed at a heating rate of 100°C/min or more in a temperature range of 450°C to 450°C for a time range of 200°C/min.
Cool at the cooling rate above.
この熱処理は成形加工性、強度への寄与が大きく、組織
の再結晶粒微細化により、並びにＭｇ、Ｃｕの固溶化に
より、ベーキング強度を向上させることを目的としたも
のである。This heat treatment greatly contributes to moldability and strength, and is intended to improve baking strength by refining the recrystallized grains of the structure and by making Mg and Cu a solid solution.
しかし、加熱速度が１００ ’Ｃ／ｍｉｎ未満では再結
晶の微細化効果が不十分であって、十分なベーキング強
度、成形性が得られない。However, if the heating rate is less than 100'C/min, the effect of recrystallization into fine particles is insufficient, and sufficient baking strength and formability cannot be obtained.
また、溶体化温度が４５０℃未満ではＭｇ、Ｃｕ等の固
溶体化や再結晶微細化が不十分となり、ベーキング強度
、成形加工性を得ることができず、また５６０℃を超え
ると共晶融解の恐れがあるので避けるべきである。また
、溶体化処理時間が１００秒を超えると同溶体化は十分
となるが、再結晶粒の粗大化が起り、成形加工性、強度
が低下すると共に、工業的製品での長時間加熱、すなわ
ち通板速度を遅くすることになるので経済的でない。Furthermore, if the solution temperature is lower than 450°C, solid solution formation and recrystallization of Mg, Cu, etc. will be insufficient, making it impossible to obtain baking strength and moldability, and if it exceeds 560°C, eutectic melting will occur. It is dangerous and should be avoided. In addition, if the solution treatment time exceeds 100 seconds, the solution treatment is sufficient, but the recrystallized grains become coarser and the moldability and strength decrease, and the long-term heating of industrial products, i.e. This is not economical because it slows down the sheet threading speed.
１〜１００秒の範囲が望ましい。A range of 1 to 100 seconds is desirable.
一方、溶体化処理後の冷却では、Ｍｇ、Ｃｕ等の固溶体
化を図り、ベーキング強度の向上、成形加工性の向上の
ために２００℃／ｍｊｎ以上の冷却速度とする必要があ
る。しかし、冷却速度が２００’Ｃ／ｍｉｎ未満ではＭ
ｇ、Ｃｕの化合物が析出し、その後のベーキング強度を
低下させるので好ましくない。なお、このような冷却速
度を得るための方法としては強制空冷や水冷却等がある
が、焼入れ時の歪の低減の観点からすると強制空冷を適
用するのが望ましい。On the other hand, in cooling after solution treatment, it is necessary to make Mg, Cu, etc. into a solid solution, and to set the cooling rate to 200° C./mjn or more in order to improve baking strength and moldability. However, if the cooling rate is less than 200'C/min, M
This is not preferable because the compound of g and Cu precipitates and reduces the subsequent baking strength. Note that methods for obtaining such a cooling rate include forced air cooling, water cooling, etc., but from the viewpoint of reducing distortion during quenching, it is desirable to apply forced air cooling.
（実施例） 次に本発明の実施例を示す。(Example) Next, examples of the present invention will be shown.
失席剣↓−
第１表に示す化学成分を有するアルミニウム合金を溶製
、鋳造して、結晶粒径が１．５ｍｍ以下で５００ｍｍ厚
の鋳塊を得た。この鋳塊に４９０℃Ｘ４ｈｒの均質化処
理を施した後、５２０〜３５０℃で板厚４ｍｍまで熱間
圧延し、続いて板厚１ｍｍまで冷間圧延（最終冷間加工
率７５％）を行った。Lost Sword↓- An aluminum alloy having the chemical components shown in Table 1 was melted and cast to obtain an ingot with a crystal grain size of 1.5 mm or less and a thickness of 500 mm. After homogenizing the ingot at 490°C for 4 hours, it was hot rolled at 520 to 350°C to a thickness of 4mm, and then cold rolled to a thickness of 1mm (final cold working rate 75%). Ta.
この板厚１ｍｍのアルミニウム合金板を加熱速度７００
℃／ｍｉｎで加熱し、溶体化処理（５３０℃×２０秒）
した後、冷却速度８００℃／ｍｉｎで冷却した。This aluminum alloy plate with a thickness of 1 mm was heated at a heating rate of 700.
Heating at °C/min and solution treatment (530 °C x 20 seconds)
After that, it was cooled at a cooling rate of 800° C./min.
熱処理後に、機械的性質、エリクセン値（Ｅｒ）及びベ
ーキング（１７５°ＣＸ２０ｍ１ｎ）後の強度について
調査した。その結果を第２表に示す。After heat treatment, mechanical properties, Erichsen value (Er), and strength after baking (175°C x 20ml) were investigated. The results are shown in Table 2.
第２表から明らかなように、本発明例Ｎａ １〜Ｎｎ２
は、比較例Ｎ（１３〜Ｎα５に比べ、ベーキング強度が
優れているばかりでなく、成形加工性（伸び、エリクセ
ン値）等も優れていることがわかる。従来合金に対して
本発明の製造プロセスを適用した比較例Ｎα３〜Ｎα４
ではベーキング強度が低く、成形加工性も劣っており、
またＣｕが多い比較例Ｎ。As is clear from Table 2, examples of the present invention Na 1 to Nn2
It can be seen that compared to Comparative Example N (13 to Nα5), not only is baking strength superior, but also moldability (elongation, Erichsen value), etc. is superior. Comparative examples Nα3 to Nα4 applying
has low baking strength and poor moldability,
Comparative example N also contains a large amount of Cu.
５は熱間圧延時に割れが発生した。In No. 5, cracks occurred during hot rolling.
［以下余白１
実施例り
前記第１表に示した化学成分を有するアルミニウム台金
Ｈａ １について、第３表に示す種々の条件（鋳塊結晶
粒サイズ、最終冷間圧延率、加熱速度、溶体化処理温度
及び時間、冷却速度）にてアルミニウム合金板を製造し
、それらの条件の及ぼす影響について調査した。その結
果を第４表に示す。[Blank below 1 Examples] Regarding the aluminum base metal Ha 1 having the chemical composition shown in Table 1 above, various conditions shown in Table 3 (ingot crystal grain size, final cold rolling rate, heating rate, solution The effects of these conditions were investigated. The results are shown in Table 4.
なお、他の条件は実施例１と同様とした。Note that other conditions were the same as in Example 1.
第４表から明らかなように、本発明例Ｎαｌはベーキン
グ強度が優れているばかりでなく、成形加工性（伸び、
エリクセン値）等も優れていることがわかる。As is clear from Table 4, inventive example Nαl not only has excellent baking strength but also moldability (elongation,
It can be seen that the Erichsen value) etc. are also excellent.
一方、第３表の条件のうち、いずれかの条件が本発明範
囲外である比較例の場合、すなわち、鋳塊結晶粒サイズ
が大きい比較例Ｎα２、最終冷間圧延率が小さい比較例
Ｎｎ ３、熱処理条件が本発明範囲外の比較例Ｎａ４〜
Ｎａ ７はいずれもベーキング後の強度が低く、成形加
工性も劣っている。On the other hand, in the case of comparative examples in which any of the conditions in Table 3 is outside the scope of the present invention, that is, comparative example Nα2 with a large ingot crystal grain size, and comparative example Nn 3 with a small final cold rolling reduction. , Comparative examples Na4 to 4 where the heat treatment conditions were outside the range of the present invention.
All of Na 7 have low strength after baking and poor moldability.
［以下余白］
（発明の効果）
以上詳述したように、本発明によれば、成形加工後のベ
ーキングにおける強度向上が要求される成形加工品に使
用されるアルミニウム合金板として、従来材の５１８２
．５０５２と同等以上の成形加工性を有し、しかもベー
キング後の強度が格段に優れているため、薄肉化が可能
となり、自動車、車両等の軽量化に寄与するところが大
きい。[Blank below] (Effects of the Invention) As detailed above, according to the present invention, the conventional material 5182 can be used as an aluminum alloy plate used in molded products that require improved strength during baking after molding.
．． It has moldability equal to or better than 5052, and its strength after baking is significantly superior, so it can be made thinner, which greatly contributes to reducing the weight of automobiles, vehicles, etc.
特許出願人 株式会社神戸製鋼所 代理人弁理士 中 村 尚Patent applicant: Kobe Steel, Ltd. Representative Patent Attorney Takashi Nakamura
Claims (1)
ｎ：０．０６〜０．６％及びＣｕ：０．３〜２．０％を
必須成分とし、更にＭｎ：０．０３〜０．５％、Ｃｒ：
０．０３〜０．３％、Ｔｉ：０．００５〜０．３％及び
Ｂ：０．０００５〜０．０５％のうちの１種又は２種以
上を含有し、残部がＡｌ及び不可避的不純物からなるＡ
ｌ合金につき、結晶粒径が１．５ｍｍ以下の鋳塊を用い
、均質化処理後、熱間圧延を行い、次いで最終の冷間加
工率を６０％以上与えて所定の板厚とし、引き続いて、
１００℃／ｍｉｎ以上の加熱速度で４５０〜５６０℃×
１００秒以下の加熱を行った後、冷却速度２００℃／ｍ
ｉｎ以上で冷却することを特徴とするベーキング強度に
優れた成形加工用アルミニウム合金の製造方法。In weight% (the same applies hereinafter), Mg: 3.0 to 5.0%, Z
n: 0.06-0.6% and Cu: 0.3-2.0% as essential components, further Mn: 0.03-0.5%, Cr:
0.03 to 0.3%, Ti: 0.005 to 0.3%, and B: 0.0005 to 0.05%, and the remainder is Al and inevitable impurities. A consisting of
For l alloy, an ingot with a crystal grain size of 1.5 mm or less is used, and after homogenization treatment, hot rolling is performed, and then a final cold working rate of 60% or more is applied to obtain a predetermined plate thickness, and then ,
450 to 560℃ at a heating rate of 100℃/min or more
After heating for 100 seconds or less, cooling rate 200℃/m
A method for producing an aluminum alloy for molding with excellent baking strength, characterized by cooling at a temperature of at least 100 mL.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16035988A JPH028353A (en) | 1988-06-27 | 1988-06-27 | Manufacture of aluminum alloy for forming excellent in baking strength |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP16035988A JPH028353A (en) | 1988-06-27 | 1988-06-27 | Manufacture of aluminum alloy for forming excellent in baking strength |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH028353A true JPH028353A (en) | 1990-01-11 |
Family
ID=15713270
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP16035988A Pending JPH028353A (en) | 1988-06-27 | 1988-06-27 | Manufacture of aluminum alloy for forming excellent in baking strength |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH028353A (en) |
Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0613959A1 (en) * | 1993-03-03 | 1994-09-07 | Nkk Corporation | An aluminium alloy sheet for use in press forming , exhibiting excellent hardening property obtained by baking at low temperature for a short period of time and a method of manufacturing the same |
| EP0616044A2 (en) * | 1993-03-03 | 1994-09-21 | Nkk Corporation | Method of manufacturing natural aging retardated aluminum alloy sheet |
| US5423925A (en) * | 1992-10-23 | 1995-06-13 | The Furukawa Electric Co., Ltd. | Process for manufacturing Al-Mg alloy sheets for press forming |
| DE10231437B4 (en) | 2001-08-10 | 2019-08-22 | Corus Aluminium N.V. | Process for producing an aluminum wrought alloy product |
-
1988
- 1988-06-27 JP JP16035988A patent/JPH028353A/en active Pending
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US5423925A (en) * | 1992-10-23 | 1995-06-13 | The Furukawa Electric Co., Ltd. | Process for manufacturing Al-Mg alloy sheets for press forming |
| EP0613959A1 (en) * | 1993-03-03 | 1994-09-07 | Nkk Corporation | An aluminium alloy sheet for use in press forming , exhibiting excellent hardening property obtained by baking at low temperature for a short period of time and a method of manufacturing the same |
| EP0616044A2 (en) * | 1993-03-03 | 1994-09-21 | Nkk Corporation | Method of manufacturing natural aging retardated aluminum alloy sheet |
| US5580402A (en) * | 1993-03-03 | 1996-12-03 | Nkk Corporation | Low baking temperature hardenable aluminum alloy sheet for press-forming |
| EP0616044A3 (en) * | 1993-03-03 | 1997-05-02 | Nippon Kokan Kk | Method of manufacturing natural aging retardated aluminum alloy sheet. |
| DE10231437B4 (en) | 2001-08-10 | 2019-08-22 | Corus Aluminium N.V. | Process for producing an aluminum wrought alloy product |
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