JP2005113242A - Method of producing aluminum alloy hot rolled sheet for resin-coated building material having excellent strength and bending workability - Google Patents
Method of producing aluminum alloy hot rolled sheet for resin-coated building material having excellent strength and bending workability Download PDFInfo
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- 238000005452 bending Methods 0.000 title claims abstract description 37
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 16
- 239000011347 resin Substances 0.000 title claims description 12
- 229920005989 resin Polymers 0.000 title claims description 12
- 239000004566 building material Substances 0.000 title claims description 9
- 238000000034 method Methods 0.000 title description 13
- 239000012535 impurity Substances 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 4
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 3
- 229910052802 copper Inorganic materials 0.000 claims abstract description 3
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 3
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 3
- 238000004519 manufacturing process Methods 0.000 claims description 25
- 239000011248 coating agent Substances 0.000 claims description 9
- 238000000576 coating method Methods 0.000 claims description 9
- 239000013078 crystal Substances 0.000 claims description 9
- 238000005098 hot rolling Methods 0.000 abstract description 16
- 238000002791 soaking Methods 0.000 abstract description 11
- 229910052742 iron Inorganic materials 0.000 abstract description 4
- 229910052751 metal Inorganic materials 0.000 abstract description 2
- 239000002184 metal Substances 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 150000002739 metals Chemical class 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 12
- 238000005266 casting Methods 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 5
- 239000000956 alloy Substances 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000005336 cracking Methods 0.000 description 3
- 230000007423 decrease Effects 0.000 description 3
- 239000000463 material Substances 0.000 description 3
- 238000001953 recrystallisation Methods 0.000 description 3
- 238000005096 rolling process Methods 0.000 description 3
- 229910018131 Al-Mn Inorganic materials 0.000 description 2
- 229910018461 Al—Mn Inorganic materials 0.000 description 2
- YCKRFDGAMUMZLT-UHFFFAOYSA-N Fluorine atom Chemical compound [F] YCKRFDGAMUMZLT-UHFFFAOYSA-N 0.000 description 2
- 238000000137 annealing Methods 0.000 description 2
- 238000005097 cold rolling Methods 0.000 description 2
- 230000000052 comparative effect Effects 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 238000009749 continuous casting Methods 0.000 description 2
- 238000007796 conventional method Methods 0.000 description 2
- 238000012937 correction Methods 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 229910052731 fluorine Inorganic materials 0.000 description 2
- 239000011737 fluorine Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 229920006395 saturated elastomer Polymers 0.000 description 2
- 238000012360 testing method Methods 0.000 description 2
- 229910010039 TiAl3 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
- 229910052791 calcium Inorganic materials 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 230000001771 impaired effect Effects 0.000 description 1
- 229910052745 lead Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000003973 paint Substances 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000010583 slow cooling Methods 0.000 description 1
- 229910052708 sodium Inorganic materials 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 229910052718 tin Inorganic materials 0.000 description 1
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Abstract
Description
この発明は、高強度かつ曲げ加工性に優れた樹脂塗装建材用アルミニウム合金熱延板の製造方法に関し、特に弗素樹脂のような高温焼付を施す樹脂塗装建材用アルミニウム合金 熱延板の製造方法に関する。 TECHNICAL FIELD The present invention relates to a method for producing an aluminum alloy hot-rolled sheet for resin-coated building materials having high strength and excellent bending workability, and particularly relates to a method for producing an aluminum alloy hot-rolled sheet for resin-coated building materials that is subjected to high-temperature baking such as fluorine resin. .
樹脂塗装建材は、最近、弗素樹脂のような高温焼付塗料を用い、かつ、90°曲げ以上の100〜180゜の厳しい曲げ加工の施工デザインとなるケースがある。そして、通常、曲げ加工を必要とする板厚は1.2〜3.0mmで、3.0mmを超えて6.0mmまでは曲げ加工をしないで施工される。
この様な用途用のアルミニウム合金板として、例えば特許文献1が挙げられる。
As an aluminum alloy plate for such a use, patent document 1 is mentioned, for example.
しかしながら、特許文献1記載の発明は、強度と135°曲げ加工では優れた効果があるものの、135°曲げ以上の曲げ加工、例えば180°の曲げ加工では割れが発生する恐れがある。
また製造工程(鋳造→均熱・加熱→熱間圧延→一次冷間圧延→中間焼鈍→二次冷間圧延→最終焼鈍)が長すぎて高エネルギー・高コストとなってしまう。
However, the invention described in Patent Document 1 has excellent effects in strength and 135 ° bending, but there is a risk of cracking in bending over 135 ° bending, for example, 180 ° bending.
In addition, the production process (casting → soaking / heating → hot rolling → primary cold rolling → intermediate annealing → secondary cold rolling → final annealing) is too long, resulting in high energy and high cost.
この発明は上記の従来技術の欠点を解消し、高温焼付塗装によっても強度(引張強さ135N/mm2以上)を損なうことなく曲げ加工性を向上したアルミニウム合金圧延板を省エネルギー・低コストで製造し得る方法を提供することを目的とする。 This invention eliminates the above-mentioned drawbacks of the prior art, and produces aluminum alloy rolled sheets with improved bending workability without sacrificing strength (tensile strength of 135 N / mm 2 or more) by high-temperature baking coating at low energy and low cost. It is an object to provide a method that can do this.
本発明者らは上記課題を解決するためにアルミニウム合金板の成分組成と鋳造後の製造条件を鋭意検討した結果、本発明を完成したものである。
すなわち本発明は、Mn:0.8〜1.5%、Fe:0.10〜0.7%を含み、さらに、Si:0.05〜0.6%、Cu:0.05〜0.5%、Mg:0.05〜0.3%、Zn:0.05〜0.5%、Cr:0.05〜0.3%、Zr:0.05〜0.2%、V:0.05〜0.2%の一種以上を含み残部不可避不純物およびAlとからなるAl合金鋳塊を、580〜640℃の範囲内の温度で均熱処理し、熱間圧延を475〜525℃の範囲内の温度で開始し、240℃以上290℃未満の範囲内の温度で終了させる層状結晶粒の熱間圧延板であって、引張強さが135N/mm2以上、導電率が48.0%IACS未満であることを特徴とする強度と曲げ加工性に優れた樹脂塗装建材用アルミニウム合金熱延板の製造方法を要旨としている。
In order to solve the above-mentioned problems, the present inventors have intensively studied the composition of the aluminum alloy sheet and the production conditions after casting, and as a result, completed the present invention.
That is, the present invention includes Mn: 0.8 to 1.5%, Fe: 0.10 to 0.7%, Si: 0.05 to 0.6%, Cu: 0.05 to 0.00. 5%, Mg: 0.05 to 0.3%, Zn: 0.05 to 0.5%, Cr: 0.05 to 0.3%, Zr: 0.05 to 0.2%, V: 0 0.05% to 0.2% of an Al alloy ingot including at least one of the inevitable impurities and Al is soaked at a temperature within a range of 580 to 640 ° C., and hot rolling is performed within a range of 475 to 525 ° C. Is a hot rolled sheet of layered crystal grains that starts at a temperature within the range and ends at a temperature within the range of 240 ° C. or more and less than 290 ° C., and has a tensile strength of 135 N / mm 2 or more and a conductivity of 48.0%. A summary of a method for producing an aluminum alloy hot-rolled sheet for resin-coated building materials excellent in strength and bending workability, characterized by being less than IACS doing.
本発明の方法は省エネルギー・低コストの製造方法で、この製造方法で得られたアルミニウム合金熱延板は、特に曲げ加工性に優れ、樹脂焼付塗装後は強度低下もなく高強度を有していることから、特に曲げ加工の厳しい135〜180゜曲げ加工を要求される樹脂焼付塗装建材として好適である。 The method of the present invention is an energy-saving and low-cost production method, and the aluminum alloy hot-rolled sheet obtained by this production method is particularly excellent in bending workability, and has high strength without strength reduction after resin baking. Therefore, it is suitable as a resin baked coating building material that requires a bending process of 135 to 180 °, which is particularly difficult to bend.
まず、本発明における化学成分の限定理由を説明する。
Mn:Mnは強度を向上する元素であり、0.8%未満ではその効果が小さく、1.5%を超えると向上しすぎて曲げ加工性が低下する。従って、Mn量は0.8〜1.5%の範囲とする。
First, the reasons for limiting chemical components in the present invention will be described.
Mn: Mn is an element that improves the strength. If the content is less than 0.8%, the effect is small. Therefore, the amount of Mn is set to a range of 0.8 to 1.5%.
Fe:Feは強度に寄与するが、鋳造時にMnと化合してAl−Mn−Fe系晶出化合物となり曲げ加工性を阻害する元素である、0.10%未満では必要強度が得られず、0.7%を超えると曲げ加工性を著しく阻害する。従って、Fe量は0.10〜0.7%の範囲とする。 Fe: Fe contributes to strength, but it is an element that combines with Mn at the time of casting to become an Al-Mn-Fe crystallization compound and inhibits bending workability, and if it is less than 0.10%, the required strength cannot be obtained, If it exceeds 0.7%, bending workability will be significantly impaired. Therefore, the amount of Fe is set to a range of 0.10 to 0.7%.
Si:Siは強度を付与する元素であるが、0.05%未満では効果が無く、0.6%を超えると強度の向上が飽和して、それ以上添加しても無駄である。従って、Si量は0.05〜0.6%の範囲とする。 Si: Si is an element that imparts strength, but if it is less than 0.05%, there is no effect, and if it exceeds 0.6%, the improvement in strength is saturated and it is useless to add more. Therefore, the Si amount is in the range of 0.05 to 0.6%.
Cu:Cuは強度を付与する元素であるが、0.05%未満では効果が無く、0.5%を超えると耐食性が劣化するので好ましくない。従って、Cu量は0.05〜0.5%の範囲とする。 Cu: Cu is an element that imparts strength, but if it is less than 0.05%, there is no effect, and if it exceeds 0.5%, corrosion resistance deteriorates, which is not preferable. Therefore, the amount of Cu is made 0.05 to 0.5% in range.
Mg:Mgは固溶して強度を向上する元素であり、0.05%未満ではその効果が小さく、0.3%を超えると向上しすぎて曲げ加工性が低下する。従って、Mg量は0.05〜0.3%の範囲とする。 Mg: Mg is an element that improves the strength by forming a solid solution. If it is less than 0.05%, its effect is small, and if it exceeds 0.3%, it is improved too much and bending workability is lowered. Therefore, the Mg amount is set in the range of 0.05 to 0.3%.
Zn:Znは強度を付与する元素であるが、0.05%未満では効果が無く、0.5%を超えると耐食性が劣化するので好ましくない。従って、Zn量は0.03〜0.5%の範囲とする。 Zn: Zn is an element imparting strength, but if it is less than 0.05%, there is no effect, and if it exceeds 0.5%, corrosion resistance deteriorates, which is not preferable. Therefore, the Zn content is in the range of 0.03 to 0.5%.
Cr:Crは強度向上に寄与する元素であるが、0.05%未満では効果が無く、0.3%を超えると巨大化合物が生成され曲げ加工性が低下する。従って、Cr量は0.05〜0.3%の範囲とする。 Cr: Cr is an element that contributes to strength improvement, but if it is less than 0.05%, there is no effect, and if it exceeds 0.3%, a giant compound is produced and bending workability is lowered. Therefore, the Cr content is in the range of 0.05 to 0.3%.
Zr,V:ZrおよびVは強度を付与する元素であるが、0.05%未満ではその効果が無く、0.2%を超えると巨大化合物が生成され曲げ加工性が低下するので好ましくない。従って、Zr量およびV量は0.05〜0.2%の範囲とする。 Zr, V: Zr and V are elements that impart strength, but if less than 0.05%, there is no effect, and if it exceeds 0.2%, a giant compound is produced and bending workability is lowered, which is not preferable. Therefore, the Zr amount and the V amount are in the range of 0.05 to 0.2%.
上記元素以外は不純物あるいは任意添加元素である。以下に任意添加元素を添加する場合の添加範囲を説明する。 Other than the above elements are impurities or optional added elements. The addition range when adding an optional additive element will be described below.
Ti,B:通常のアルミニウム合金においては、鋳塊の微細化のために、Ti単独もしくはTiとBを複合添加することが行なわれている。本発明においてもTi単独もしくはTiとBを複合添加しても良い。その場合、Ti量は0.005%未満では効果が無く、0.15%を超えると初晶TiAl3が晶出して曲げ加工性が阻害されるので、Ti量は0.005〜0.15%の範囲とする。また、TiとともにBを添加する場合のB量は、1ppm未満では効果が無く、500ppmを超えるとTiB2が生成して曲げ加工性が阻害されるので、B量は1〜500ppmとする。 Ti, B: In ordinary aluminum alloys, Ti alone or a combination of Ti and B is added to make the ingot finer. Also in the present invention, Ti alone or Ti and B may be added in combination. In that case, if the amount of Ti is less than 0.005%, there is no effect, and if it exceeds 0.15%, primary TiAl3 crystallizes and bending workability is hindered, so the amount of Ti is 0.005 to 0.15%. The range. Further, when adding B together with Ti, the amount of B is less than 1 ppm, and if it exceeds 500 ppm, TiB 2 is generated and bending workability is hindered, so the amount of B is set to 1 to 500 ppm.
Be:Beは、溶湯酸化の防止のために添加する場合があるが、本発明においても添加しても良い。その場合のBe量は、1ppm未満では効果が無く、500ppmを超えると効果が飽和して、それ以上添加することは無駄である。従って、Be量は1〜500ppmの範囲とする。 Be: Be may be added to prevent oxidation of the molten metal, but it may also be added in the present invention. In that case, if the amount of Be is less than 1 ppm, there is no effect, and if it exceeds 500 ppm, the effect is saturated, and it is useless to add more. Therefore, the amount of Be is in the range of 1 to 500 ppm.
また、アルミニウム地金に起因するNa、Ca、Pb、Bi、Ga、Sn、Ni等の不純物は各々単独で200ppm未満に抑えることが好ましい。 Moreover, it is preferable to suppress each impurity, such as Na, Ca, Pb, Bi, Ga, Sn, and Ni, originating from the aluminum ingot to less than 200 ppm.
次に、アルミニウム合金圧延板の製造方法について工程順に説明する。
[鋳造]鋳造法は特に限定されず、常法によって鋳塊を作ればよいが、DC鋳造法(半連続鋳造法)が望ましい。
Next, the manufacturing method of an aluminum alloy rolled sheet is demonstrated in order of a process.
[Casting] The casting method is not particularly limited, and an ingot may be formed by a conventional method, but a DC casting method (semi-continuous casting method) is desirable.
[均熱処理]均熱処理は580〜640℃の高温(導電率的にAl-Mn系析出物の析出ピークを過ぎて低下の傾向を示す再固溶の温度領域)で行い、再結晶温度を適度に低めて、熱間圧延終了板の終了温度による軟化を適度に抑制するために行う。
均熱温度が580℃未満では粗大なAl−Mn系析出物の数が不足して導電率が上昇することで再結晶温度も上昇し、熱間圧延終了板は高強度となって曲げ加工性が低下しやすく、640℃を超えると溶解の恐れがある。従って、均熱温度は580〜640℃の範囲とする。また、保持時間は温度にもよるが1〜24hrとすれば本発明の目的は達成し、本発明の熱間圧延終了板の導電率は48.0%IACS未満となる。
[Soaking process] The soaking process is performed at a high temperature of 580 to 640 ° C. (re-solution temperature range in which conductivity tends to decrease past the precipitation peak of the Al—Mn-based precipitate), and the recrystallization temperature is moderate. In order to moderately suppress softening due to the end temperature of the hot rolled end plate.
If the soaking temperature is less than 580 ° C, the number of coarse Al-Mn-based precipitates is insufficient and the conductivity increases, so the recrystallization temperature also rises, the hot-rolled finished plate becomes high strength, and the bending workability decreases. It is easy to do, and when it exceeds 640 ° C, there is a risk of dissolution. Accordingly, the soaking temperature is in the range of 580 to 640 ° C. Further, if the holding time is 1 to 24 hours depending on the temperature, the object of the present invention is achieved, and the electrical conductivity of the hot-rolled finished plate of the present invention is less than 48.0% IACS.
[加熱処理および熱間圧延]熱間圧延終了段階の終了までの3パスは1パス当たり40〜60%の圧延率で行い、熱間圧延終了温度を240℃以上290℃未満の範囲内に抑え易くするために熱間圧延開始温度は475〜525℃の範囲内とする。熱間圧延のための加熱はこの熱間圧延条件を満たすように行う。ただし、加熱処理は、均熱処理後の鋳塊が475〜525℃の範囲内に徐冷されるのを待って熱間圧延を行う場合は省略してもよい。 [Heat Treatment and Hot Rolling] Three passes until the end of the hot rolling end stage are performed at a rolling rate of 40 to 60% per pass, and the hot rolling end temperature is kept within a range of 240 ° C. or higher and lower than 290 ° C. In order to facilitate, the hot rolling start temperature is set within a range of 475 to 525 ° C. Heating for hot rolling is performed so as to satisfy this hot rolling condition. However, the heat treatment may be omitted when hot rolling is performed after the ingot after soaking has been gradually cooled within the range of 475 to 525 ° C.
[熱間圧延終了温度]熱間圧延終了温度は、弗素樹脂焼付塗装条件(240〜280℃×20min)以上の条件と規定する。こうすることにより弗素樹脂焼付塗装後の強度低下や変形は起こらない。熱間圧延終了温度が240℃未満では高強度になりすぎて曲げ加工性が低下しやすく、290℃以上では全面または部分的再結晶を起こして強度低下を招き好ましくないので熱間圧延終了温度は240℃以上290℃未満の範囲内とする。さらに、熱間圧延終了板は最終パスの出側でコイル状に巻き上げてから冷却するが、240℃(弗素樹脂焼付塗装温度の下限)までは30℃/hr以下の徐冷とすることが好ましい。 [Hot rolling end temperature] The hot rolling end temperature is defined as a condition of fluororesin baking coating conditions (240 to 280 ° C x 20 min) or more. By doing so, there is no reduction in strength or deformation after fluororesin baking coating. If the hot rolling end temperature is less than 240 ° C., the strength becomes too high and bending workability tends to decrease, and if it is 290 ° C. or higher, the entire surface or partial recrystallization is caused and the strength is lowered. It is within the range of 240 ° C. or more and less than 290 ° C. Further, the hot-rolled plate is cooled after being coiled on the exit side of the final pass, and is preferably gradually cooled to 30 ° C./hr or less up to 240 ° C. (lower limit of the fluororesin baking coating temperature). .
また、室温まで冷却後、ローラーレベラー、ストレッチャー等で歪矯正を行なうが、この場合、樹脂焼付塗装前の強度が若干向上し、樹脂焼付塗装後は低下するが歪矯正前の強度以下になることはなく、本発明の効果を妨げない。 In addition, after cooling to room temperature, distortion correction is performed with a roller leveler, stretcher, etc. In this case, the strength before resin baking coating is slightly improved, and the strength after resin baking coating is reduced, but is less than the strength before distortion correction. It does not interfere with the effects of the present invention.
表1の合金A〜Gについて、常法に従ってDC鋳造法(半連続鋳造法)により鋳造し、厚さ450mm×幅1200mm×長さ3000mm)の鋳塊を得た。 Alloys A to G in Table 1 were cast by a DC casting method (semi-continuous casting method) in accordance with a conventional method to obtain an ingot having a thickness of 450 mm × width of 1200 mm × length of 3000 mm.
得られた鋳塊に対し、表2の製造番号1〜10に示す条件で均熱後熱間圧延を施して(終了までの3パスは1パス当り40〜60%の圧延率)厚さ3.0mmとし(ただし、製造番号2は6.0mm、製造番号3は1.2mm)、240℃までの徐冷は30℃/hr以下で行った。
そして、各熱延板について強度と曲げ加工性と導電率と結晶粒の形状を調べた。強度は引張試験で引張強さを測定し、曲げ加工性は180°曲げ(内側曲げ半径0mmR)試験にて割れの有無を調べ、導電率はSIGMATEST(ドイツ製導電率測定器 Typ2.067)で測定した。また、結晶粒の形状は圧延表面の結晶粒を25〜50倍の顕微鏡で観察し、アスペクト比(結晶粒の最大長さ÷結晶粒の最小長さ)の平均が5.0以上を層状とし、5.0未満を粒状とした。その結果を表2中に併せて示す。
The obtained ingot was subjected to hot rolling after soaking under the conditions shown in production numbers 1 to 10 in Table 2 (3 passes until the end was a rolling rate of 40 to 60% per pass), thickness 3 It was set to 0.0 mm (however, production number 2 was 6.0 mm and production number 3 was 1.2 mm), and slow cooling to 240 ° C. was performed at 30 ° C./hr or less.
Each hot-rolled sheet was examined for strength, bending workability, electrical conductivity, and crystal grain shape. Strength is measured by tensile test, bending workability is checked for cracking by 180 ° bending (inner bending radius 0mmR) test, conductivity is SIGMATEST (German conductivity meter Typ2.067) It was measured. In addition, the shape of the crystal grains is observed by observing the crystal grains on the rolling surface with a microscope of 25 to 50 times, and the average aspect ratio (maximum length of crystal grains ÷ minimum length of crystal grains) is 5.0 or more. , Less than 5.0 was granular. The results are also shown in Table 2.
以下、個々の結果について説明する。
製造番号1〜3の材料は、いずれも成分組成および製造プロセスの両者が本発明で規定する条件を満たす発明例であり、表2に示すように結晶粒は層状で導電率は48.0%IACS未満、引張強さは135N/mm2以上の高強度を示し、曲げ加工性は180°曲げ試験でも割れが発生しない、強度と曲げ加工性に優れた材料となっていることが明らかである。
Hereinafter, individual results will be described.
The materials of production numbers 1 to 3 are invention examples in which both the component composition and the production process satisfy the conditions stipulated in the present invention. As shown in Table 2, the crystal grains are layered and the conductivity is 48.0%. It is clear that the material is superior in strength and bending workability with less than IACS, tensile strength of 135 N / mm 2 or higher, and bending workability without cracking even in a 180 ° bending test. .
一方、製造番号4〜6の材料は、本発明で規定する成分組成条件は満たすが、製造プロセス条件の一部を満たさない比較例である。
製造番号4は本発明の規定する均熱条件は満たすが熱間圧延開始温度が規定範囲よりも高すぎたため、終了温度が290℃以上の高温となり結晶粒が粒状となってしまって、曲げ加工性は良好であるが引張強さは135N/mm2以下の低強度となってしまった。
製造番号5は本発明の規定する均熱条件は満たすが熱間圧延開始温度が規定範囲を下回ったため、終了温度が240℃未満の低温となってしまい、高強度であるが曲げ加工性は低下してしまった。
製造番号6は本発明の規定する均熱温度範囲よりも低すぎたため熱間圧延条件は満たしても導電率が48.0%以上となってしまって軟化不足となり、高強度であるが曲げ加工性は低下してしまった。
On the other hand, the materials of production numbers 4 to 6 are comparative examples that satisfy the component composition conditions defined in the present invention but do not satisfy a part of the production process conditions.
Production No. 4 satisfies the soaking condition defined in the present invention, but the hot rolling start temperature is too higher than the specified range, so the end temperature becomes higher than 290 ° C., and the crystal grains become granular, and bending processing is performed. The tensile strength was as low as 135 N / mm 2 or less.
Production No. 5 satisfies the soaking condition defined in the present invention, but the hot rolling start temperature falls below the specified range, so the end temperature becomes a low temperature of less than 240 ° C., and the strength is high but the bending workability is lowered. have done.
Since the production number 6 was too lower than the soaking temperature range defined in the present invention, even if the hot rolling conditions were satisfied, the electrical conductivity was 48.0% or more, and the softening was insufficient and the bending strength was high. Sex has declined.
また、製造番号7〜10は本発明で規定する製造プロセス条件は満たすが、成分組成条件を満たさない比較例である。
製造番号7はMn量が本発明で規定する成分範囲よりも低い合金Dを用い、製造番号8はMn量が本発明で規定する成分範囲よりも高い合金Eを用いたもので、前者はMn量が少ないため曲げ加工性は良好であるが引張強さは135N/mm2以下の低強度となり、後者はMn量が多いため高強度になりすぎて曲げ加工性が低下してしまった。
製造番号9はFe量とSi量が本発明で規定する成分範囲よりも低い合金Fを用い、製造番号10はFe量が本発明で規定する成分範囲よりも高い合金Gを用いたもので、前者はFe量とSi量が少ないため曲げ加工性は良好であるが引張強さは135N/mm2以下の低強度となり、後者はFe量が多いため高強度になってしまったことと、Al−Mn−Fe系晶出化合物のサイズが大となったことで曲げ加工性は低下した。
Production numbers 7 to 10 are comparative examples that satisfy the production process conditions defined in the present invention but do not satisfy the component composition conditions.
The production number 7 uses an alloy D whose Mn amount is lower than the component range defined in the present invention, and the production number 8 uses an alloy E whose Mn amount is higher than the component range defined in the present invention. Since the amount is small, the bending workability is good, but the tensile strength is as low as 135 N / mm 2 or less, and the latter is too strong because the amount of Mn is large, and the bending workability is lowered.
The production number 9 is an alloy F in which the Fe amount and the Si amount are lower than the component range defined in the present invention, and the production number 10 is an alloy G in which the Fe amount is higher than the component range defined in the present invention. The former is good in bending workability due to the small amount of Fe and Si, but the tensile strength is low strength of 135 N / mm 2 or less, and the latter is high strength due to the large amount of Fe, Al Bending workability was reduced by increasing the size of the -Mn-Fe crystallization compound.
本発明によるアルミニウム合金圧延板を特に高温の焼付塗装が必要な弗素等の樹脂塗装建材(カーテンウォールや内外装建材等)に使用することによって、高強度を要する厳しい曲げ加工の施工デザインが可能となる。
By using the aluminum alloy rolled sheet according to the present invention for resin-coated building materials (curtain walls, interior / exterior building materials, etc.) such as fluorine that require particularly high-temperature baking coating, it is possible to design constructions for severe bending work that requires high strength. Become.
Claims (1)
Mn: 0.8 to 1.5% (mass%, the same shall apply hereinafter), Fe: 0.10 to 0.7%, Si: 0.05 to 0.6%, Cu: 0.05 to 0.5%, Mg: 0.05 to 0.3%, Zn: 0.05 to 0.5%, Cr: 0.05 to 0.3%, Zr: 0.05 to 0.2%, V : 0.05% to 0.2% of one or more Al alloy ingots including the inevitable impurities and Al are soaked at a temperature in the range of 580 to 640 ° C, and hot rolled to 475 to 525 ° C. A hot rolled sheet of layered crystal grains starting at a temperature in the range of 240 ° C. and less than 290 ° C., having a tensile strength of 135 N / mm 2 or more and an electrical conductivity of 48.0. The manufacturing method of the aluminum alloy hot-rolled sheet for resin coating building materials excellent in the intensity | strength and bending workability characterized by being less than% IACS.
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JP2006322035A (en) * | 2005-05-18 | 2006-11-30 | Furukawa Sky Kk | Rolled sheet of aluminum alloy for painted roof material and manufacturing method therefor |
WO2022127022A1 (en) * | 2020-12-17 | 2022-06-23 | 广东和胜工业铝材股份有限公司 | Aluminum alloy, and preparation method therefor and application thereof |
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JP2006322035A (en) * | 2005-05-18 | 2006-11-30 | Furukawa Sky Kk | Rolled sheet of aluminum alloy for painted roof material and manufacturing method therefor |
WO2022127022A1 (en) * | 2020-12-17 | 2022-06-23 | 广东和胜工业铝材股份有限公司 | Aluminum alloy, and preparation method therefor and application thereof |
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