JPH02235586A - Al clad steel sheet - Google Patents
Al clad steel sheetInfo
- Publication number
- JPH02235586A JPH02235586A JP5579789A JP5579789A JPH02235586A JP H02235586 A JPH02235586 A JP H02235586A JP 5579789 A JP5579789 A JP 5579789A JP 5579789 A JP5579789 A JP 5579789A JP H02235586 A JPH02235586 A JP H02235586A
- Authority
- JP
- Japan
- Prior art keywords
- core material
- layer
- steel sheet
- clad steel
- thickness
- 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.)
- Granted
Links
- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 61
- 239000010959 steel Substances 0.000 title claims abstract description 61
- 239000011162 core material Substances 0.000 claims abstract description 45
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 18
- 239000000956 alloy Substances 0.000 claims abstract description 18
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 14
- 229910000655 Killed steel Inorganic materials 0.000 claims abstract description 11
- 238000003466 welding Methods 0.000 claims abstract description 7
- 229910052751 metal Inorganic materials 0.000 claims abstract description 6
- 239000002184 metal Substances 0.000 claims abstract description 6
- KRVSOGSZCMJSLX-UHFFFAOYSA-L chromic acid Substances O[Cr](O)(=O)=O KRVSOGSZCMJSLX-UHFFFAOYSA-L 0.000 claims abstract description 4
- AWJWCTOOIBYHON-UHFFFAOYSA-N furo[3,4-b]pyrazine-5,7-dione Chemical compound C1=CN=C2C(=O)OC(=O)C2=N1 AWJWCTOOIBYHON-UHFFFAOYSA-N 0.000 claims abstract description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 3
- 239000010410 layer Substances 0.000 claims abstract 7
- 229910018084 Al-Fe Inorganic materials 0.000 claims abstract 3
- 229910018192 Al—Fe Inorganic materials 0.000 claims abstract 3
- 239000011247 coating layer Substances 0.000 claims abstract 3
- 238000005096 rolling process Methods 0.000 abstract description 22
- 229910052782 aluminium Inorganic materials 0.000 abstract description 14
- 239000011248 coating agent Substances 0.000 abstract description 5
- 238000000576 coating method Methods 0.000 abstract description 5
- 230000007797 corrosion Effects 0.000 abstract description 5
- 238000005260 corrosion Methods 0.000 abstract description 5
- 229910052799 carbon Inorganic materials 0.000 abstract description 4
- 238000007747 plating Methods 0.000 abstract description 4
- 238000010306 acid treatment Methods 0.000 abstract description 3
- 238000005304 joining Methods 0.000 abstract description 3
- 238000005097 cold rolling Methods 0.000 abstract description 2
- 239000000463 material Substances 0.000 description 14
- 230000000052 comparative effect Effects 0.000 description 8
- 229910001327 Rimmed steel Inorganic materials 0.000 description 7
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 7
- 239000007789 gas Substances 0.000 description 7
- 238000012360 testing method Methods 0.000 description 7
- 239000011651 chromium Substances 0.000 description 6
- 238000000034 method Methods 0.000 description 5
- 238000001953 recrystallisation Methods 0.000 description 5
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 4
- 238000010438 heat treatment Methods 0.000 description 4
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 4
- HEMHJVSKTPXQMS-UHFFFAOYSA-M Sodium hydroxide Chemical compound [OH-].[Na+] HEMHJVSKTPXQMS-UHFFFAOYSA-M 0.000 description 3
- 238000000137 annealing Methods 0.000 description 3
- 238000005238 degreasing Methods 0.000 description 3
- 238000009792 diffusion process Methods 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910000640 Fe alloy Inorganic materials 0.000 description 2
- 229910015372 FeAl Inorganic materials 0.000 description 2
- 230000015572 biosynthetic process Effects 0.000 description 2
- 239000010432 diamond Substances 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000000465 moulding Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 238000005554 pickling Methods 0.000 description 2
- 238000005498 polishing Methods 0.000 description 2
- 238000000992 sputter etching Methods 0.000 description 2
- 230000003746 surface roughness Effects 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- 229910001209 Low-carbon steel Inorganic materials 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910001295 No alloy Inorganic materials 0.000 description 1
- 239000004411 aluminium Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 238000005253 cladding Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 210000004709 eyebrow Anatomy 0.000 description 1
- 238000007654 immersion Methods 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 238000004519 manufacturing process Methods 0.000 description 1
- 238000001000 micrograph Methods 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052760 oxygen Inorganic materials 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052717 sulfur Inorganic materials 0.000 description 1
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B32—LAYERED PRODUCTS
- B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
- B32B15/00—Layered products comprising a layer of metal
- B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
- B32B15/012—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of aluminium or an aluminium alloy
Landscapes
- Pressure Welding/Diffusion-Bonding (AREA)
- Laminated Bodies (AREA)
Abstract
Description
【発明の詳細な説明】
〔産業上の利用分野゛１
本発明はＡｌクラッド鋼板に間し、より詳しくは加工性
に優れたＡｌクラソドＡｌキルト鋼板に閲する．
〔従来技術〕
Ａｌクラッド鋼板は、Ａｌの優れた耐食性、耐熱性、高
光熱反射特性と鋼の強度、加工性を兼ね備えた有用な材
料である．要求特性により表面のＡｌ層を純Ａｌ．Ａｌ
−Ｍｇ系合金、 Ａｌ−Ｓｔ系合金、その他の合金と使
い分けることにより、用途に適した材料が提供される．
しかし、従来、種々の制約から、Ａｌ層の密着性とあ
る程度の加工性を有するＡｌクラッド鋼板は窒素添加リ
ムド鋼を芯材とするものでしか得られなかった．また、
製法も工程が複諏であり、特性、経済性の点で多用され
るに至っていない．
従来、Ａｌクラッド鋼板は、Ａｌ板と鋼板が変形抵抗差
が著しく異なるため，また、鋼板の熱閏圧延温度ではＡ
ｌ板が溶融してしまうため、冷間圧延法により製遺され
ていた．この方法はＡｌ板と鋼板を重ね合わせて圧延圧
接した俺、拡散熱処理を行い、更に、調質圧延の後製品
となる． また、板厚寸法精度の高い製品を得るために
は、拡散熱！３１後、仕上げ圧延と軟化弊処理が必要で
ある．Ａｌと鋼板の圧接圧延工程では剥離の生じない程
度に接合するには高圧下率で圧延する必要があり、通常
、 ３０〜７０％の圧下率で圧延される．このため ａ
板の加工性を回復するためには、再結晶軟化熱処理が不
可欠である，然るに，Ａｌと鋼板は加熱すると容易に脆
い合金層を形成するため、加工するとＡｌと鋼板の界面
の合金層で剥離を生じる．このため、再結晶温度におい
て合金層形成の少ない窒素添加リムド鋼板が芯材として
用いられ（例えば特公昭６３−１１９８１＞、再結晶場
度下限にて軟化熱処理がおこなわれる．
（発明が解決しようとする課題）
然るに、従来の窒素添加リムド鋼板を芯材としたＡｌク
ラッド鋼板は、
（１）芯材がリムド鋼であるために不可避な介在物が多
く、過闇な加工をすると割れを生ずる頻度が高い．
（２）芯材がリムド鋼くインゴット材）であるため、漏
折による材質の均一性が悪い．（３）圧接時の圧下率が
高いため、Ａ＋と鋼板の界面の凹凸が激しくなり、被Ｎ
Ａｌ層の厚みの均一性が悪い．
（４）再結晶焼きなまし温度を十分に高くすることがで
きないため、また多量の窒素添加を要するため芯材が硬
い
等の欠点があった．
また、従来の東遣方法でＡｌキルド鋼板を芯材としてＡ
ｌクラッド鋼板を製造すると熱処理時に接合界面にＡｌ
−Ｆｅ合金層が形成され、加工時に剥離を生じて実用に
耐足ない，
本発明の目的は、前記した従来技術の欠点を解消し、加
工性に帰れ、かつ被１’ｌＡｌ肩厚みの均一性の良いＡ
ｌクラフド鋼板を提供することにある．（！１題を解決
するための手段）
本発明の妾旨は、芯材として非金属介在物が少なく、材
質の均一性に優れ、加工性の良好なＡｌキルト鋼板を芯
材とし、ＡｌもしくはＡｌ合金板が調質圧延程度の圧下
率で圧延圧接されて成るＡｌクラソドＩＩ４板である．
すなわち本発明は、Ｃ：０．ＯＯ１〜０．１重量％、Ａ
ｌ＋０．０２〜０ １重量％を含む、加工性の優れた極
低炭素Ａｌキルト鋼板が芯材であり、厚み比率・ ３〜
７５％の厚みのＡｌまたはＡｌ合金板を鋼板の圧下率：
０．１〜３．０％で圧延接合され、接合界面には合金層
が介在せず、Ａｌ層の厚み均一性の良い、加工性の優れ
たＡｌクラッド鋼板を提供する．
以下に本Ａｌクラッド鋼板に使用する鋼板の成分につい
て述べる．加工性を確保するため上限Ｃは０．１重量％
以下が好ましく、下限は、Ｃを０００１重量％未満にす
るにはコストが高くなり過ぎて経済上好ましくない事か
ら，ｏ．ｏｏｔ重量％以上とした．
Ａｌは０．０２重量％より少ないと、脱酸が十分となら
ず酸化物系の介在物が増加し加工性が悪くなる．また０
． １重量％を越えると、焼鈍工程において雰囲気中
の窒素を吸収し硬度が高くなり加工性が悪くなる．従っ
てＡｌ成分は０．０２−０１重量％とじな．低炭素鋼板
は通常焼鈍後，ストレッチャーストレインの防止のため
調質圧延により３％以下の圧下率で圧延される．圧下率
が３％を越えると加工硬化のため鋼板の加工性は劣化す
る． また、Ａｌクラッド鋼板全体の加工性、Ａｌが鋼
よりも延性に優れているため、芯材である鋼の加工性に
よりきまる． このことから、圧接圧延の圧下率は３％
以下にすることが好ましい．芯材の強度を確保するため
に３％以上に圧延するのはさしつかえないが加工性が劣
化する．また、Ａｌと鋼板の界面に脆い合金層が介在す
る場合、加工するとＡｌと鋼板の界面の合金層で剥離を
生じる，＾■とＦｅの固柑反応により形成されるＦｅ
−Ａｌ合金層はＦｅＡｌｉ． ＦｅａＡｌｓ． Ｆ
ｅＡｌｓ＊があり、 主たる相はＦｅ２Ａｌｓと考えら
れている．このＦｅｔＡｌａはビッカース硬度で８７０
〜１０２０Ｈｖと極めて硬く、 脆いため、加工により
容易に破壊され、被覆Ａｌ層は剥離する．更に、この合
金層形成時にＡｌとＦｅの拡散速度の違いによるカーケ
ンダル効果のためＡｌ層と合金層の界面に空孔を形成し
接合欠陥になる，Ｆｅ−Ａｌ合金層は４ ０ ０’Ｃ以
下では長時間加熱しても形成されないが、Ｆｅの再結晶
温度（５００〜５５０°Ｃ》以とに加熱すると短時間で
成長する．
また、本Ａｌクラッド鋼板の片面に１．０〜１０．
０ｇ／ｍ２の鍋をめっきすることにより耐食性の優れた
シームレス缶用Ａｌクラッドｓ仮を提供することができ
，片面に３０〜２ ０ ０ ｍ ｇ ／ ｍ２の金属Ｏ
ｒと５〜３０ｍｇ／ｍ’の酸化Ｃｒ層を形成する電解ク
ロムＩｔ！処理を施すことにより耐食性が優れ、Ａｌイ
ージーオープン缶蕾と同等の開口性を有するイージーオ
ーアン缶菱用Ａｌクラッド鋼板を１１供することができ
る．
（実施例）
実施例１
０、 ２７ｍｍ厚．０．０５１１ 量％Ｃ． ０
． Ｏ６ｊ１量％Ａｌのパンケーキタイプの結晶組
織を有するＡ！キルド鋼板の芯材と板厚３０μの高純度
アルミの接合面を５ Ｘ Ｉ Ｏ−’ＴｏｒｒのＡｒガ
ス中で約２０００オングストロームイオンエッチングし
重ね合わせて、常温、 ２ Ｘ １ ０−＠Ｔｏｒｒの
真空中で＃Ｉｌ板の圧下率１％で圧延圧接し、Ａｌ層の
厚み比率１０％のＡｌキルド鋼を芯材としＡｌ層と芯材
の界面にＦｅ−Ａｌ合金層が介在しないＡｌクラッド鋼
板を製造し試験に供した． （合金層の有無は断面を研
磨し光学１１１１１１ｆｉ、走査型電子ｗ４微鏡により
調査した．第４図の断ｉＩ謂ＦＲ鋪写真に示すように合
金層は介在していない．
実施例２
実施例１のＡｌクラッド鋼板のＡｌを被慣していない片
面に通常の脱脂、酸洗処Ｆ！後，フエロスタンめつき２
谷にて２． ８ｇ／ｍ２の絹をめっきを施し、ＤＩ缶
（絞りーしごき缶）成形試験に供した．
のＡｌキルド＃ｌＷを芯材と、厚さ５０μの高純度アル
ミの債合する面を５ Ｘ １ ０−’ＴｏｒｒのＡｒガ
ス中で約３０００オングストロームイオンエッチングし
、重ね合わせて、常温、 ２ Ｘ １０−’Ｔｏｒｒの
真空中で鋼板の圧下率３％で圧延圧接し．Ａｌの厚み比
率２０％のＡｌキルド鋼を芯材とし，Ａｌ眉と芯材の界
面にＦｅ−Ａｌ合金層が介在しないＡｌクラッド鋼板を
製造した．このＡｌクラッド鋼板のＡｌ１１１ｉｐｌし
ていない片面に１２０ｍｇ／ｍ’の金属Ｃｒと１５ｍｇ
／ｍ２の酸化Ｃｒ層を形成する通常の電解クロム酸処理
を施し、イージーオープン缶董成形試験に供した．
Ａｌキルド鋼板の芯材と、板厚１ ７５ｍｍの３００４
（ＡＡ記号）アルミ合金の接合面を８Ｘ１０−３Ｔｏｒ
ｒのＡｒガス中で約３０００オングストロームイオンエ
ッチングし、Ａｌ合金捩、鋼板、 Ａｌ合金板と重ね、
常温、 ２ｘ１０−％Ｔｏｒｒの真空中で鋼板の圧下率
１％で両面に圧延圧接し、Ａｌキルト鋼を芯材とし、厚
み比率７０％（３５＋３５％）のＡｌ＝Ｍｎ−Ｍｇ系合
金を圧延被覆し、芯材とＡｌ合金の界面にＦｅ−Ａｌ合
金層が介在しないＡｌクラッド鋼板を製造し試験に供し
た．Ａｌキルド鋼板の芯材と， ６０μ厚の高純度アル
ミ板の接合面を５ Ｘ １ ０−”ＴｏｒｒのＡｒガス
中で約２０００オングストロームイオンエッチングし重
ね合わせて、常温、 ２ Ｘ １ ０−’Ｔｏｒｒの真
空中で鋼板の圧下率５０％で圧延圧接し、Ａｌ層の厚み
比率１０％のＡｌキルド鋼を芯材としＡｌ層と芯材の界
面にＦｅ−Ａｌ合金層が介在しないＡｌクラッド鋼板を
製造し試験に供した．
と板厚３０μの高純度アルミの接合面を５Ｘ１０−”Ｔ
ｏｒｒのＡｒガス中で約２０００オングストロームイオ
ンエッチングし重ね合わせて、常温， ２Ｘ１ ０−
’Ｔｏｒｒの真空中で鋼板の圧下率１％で圧延圧接し、
Ａｉ層の厚み比率１０％のリムド鋼を芯材としＡｌ層と
芯材の界面にＦｅ−Ａｌ合金層が介在しないＡｌクラソ
ド鋼板を要遣し、Ａｌを被覆していない片面に通常の脱
脂、酸洗処理接、フェロスタンめっき浴にて２．８ｇ／
ｍ”の錫をめっきを施し、ＤＩ缶（ｒｌり−しごき缶）
成形試験に供 した．
材と、厚さ５０μの高純度アルミの接合する面を５ Ｘ
Ｉ． Ｏ−’ＴｏｒｒのＡｒガス中で約３０００オン
グストロームイオンエッチングし．！ｌね合わせて、常
温、 ２ Ｘ １ ０−５Ｔｏｒｒの真空中で鋼板の圧
下率３％で圧延圧接し，Ａｔの厚み比率２０％のＡｌキ
ルド鋼を芯材とし． Ａｌ層と芯材の界面にＦｅＡｌ
合金層が介在しないＡｌクラ−ｌド鋼板を製造した．こ
のＡｌクラッド鋼板のＡ＋１ｆｆＬでいない片面に１
２ ０ ｍ ｇ ／ ｍ ’の金属Ｃｒと１５ｍｇ／ｍ
２の酸化Ｃｒ層を形成する通常の電解クロム酸処理を施
し、イージーオープン缶菱成形試１こ供した．
のＡｌキルト鋼板の芯材と板厚３０μの高純度アルミの
接合面を５ Ｘ １ ０−’ＴｏｒｒのＡｒガス中で約
２０００オングストロームイオンエッチングし重ね合わ
せて、常温、２ Ｘ Ｉ Ｏ−’Ｔｏｒｒの真空中で鋼
板の圧下率１％で圧延圧接し， ５５０℃で５時間熱処
理を施し、八１層の厚み比＄ １ ０ ％のＡｌキルド
鋼を芯材としＡｌ層と芯材の界面にＦｅ−Ａｌ合金層が
介在するＡｌクラッド鋼板を製造し試験に供した． （
合金層の有無は断面を研磨し光字ｌｉｆｔ隊鑓、 走査
型電子顕微鋪により調査した． ）（Ａ Ｉ−Ｆｅ合金
層あり）
実施例１と比較例１のＡｌクラッド＃ｌｌ板の表面Ａｌ
層を７５℃の５％ＮａＯＨ溶液に浸ぜ責して溶解除去し
た後、表面粗さ計により表面１口フイル相度を測定した
．結果は第１表と第１図に示す様に、実施例１は接合前
の鋼板の粗度とほぼ同じであるが、比１１は圧下率が高
いため凹凸が激しく，Ａｌ層の薄い部分は厚い部分の１
／２以下となっている．この様に、圧下率の高いものは
表面１Ｉｌ覆Ａｌ層の厚み変動が大きい．
実１１と比較例２のＡｌクラッド鋼板をＡｌ層を内面に
して深絞り成形によりカップに成形し、その後、缶壁厚
みが１００μ、缶フランジ部２の厚みが１６０μになる
ようにしごき加工により２５０ｍｌ用シームレス缶１に
成形し，第２図に示すような缶を作った．この缶をロー
ル成形によりフランジ部の口広げ加工を行いフランジ割
れを検査した．その結果、比較例２の材料を用いた缶で
は、 １０００缶のうち１０缶の割れが認められたが実
施例２の材料を用いた缶では１０００缶の加工では割れ
は認められなかった．
実１１と比較例３．のＡｌクラ・ソド鋼板をＡｌ層を内
面にして第３図に示す２０２リキドボアタイ１のイージ
ーオープン缶蓋に加工した この加工では、 タブ６を
取り付けるリベット加工部５が過醜な加工で大型介在物
が存在すると割れが発生する．比較例３の材料でつくっ
た菱では２０００個中６個の割れが認められた．これに
対して，実施例３の材料で作った菱では割れは認められ
なかった．比較例３の材料で作った蕾の割れは材料の圧
延方向に平行で、割れ部の分析結果Ｍｎ．Ｏ、Ｓが検出
され、介在物の多いリムド鋼は実用に適さない．
実施例４と比較例４のＡｌクラッド＃ｌｌＩ板を山田式
深絞り試験機にてカップ成形を行なった．この結果、比
較例４の材料では合金層とＡｌ層の界面にてＩｌｌが生
じていたが実施例４の材料では剥離は認められなかった
．
［発明の効果］
以上詳述したように本発明によれば、Ａｌの耐食性、表
面特性とＡｌキルト鋼の優れた加工性を兼ｂ儂えたＡｌ
クラγド鋼板を提供することができることから、その工
業的な価値は極めて大きい．DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field 1] The present invention relates to Al-clad steel sheets, and more specifically to Al-clad Al-quilted steel sheets with excellent workability. [Prior Art] Al-clad steel sheet is a useful material that combines the excellent corrosion resistance, heat resistance, and high light and heat reflection properties of Al with the strength and workability of steel. Depending on the required characteristics, the surface Al layer may be made of pure Al. Al
- By using Mg-based alloys, Al-St-based alloys, and other alloys, materials suitable for various applications can be provided.
However, due to various constraints, Al-clad steel sheets with Al layer adhesion and a certain degree of workability could only be obtained using nitrogen-added rimmed steel as a core material. Also,
The manufacturing method involves multiple steps, and it has not been widely used due to its characteristics and economic efficiency. Conventionally, Al-clad steel sheets have been manufactured because the difference in deformation resistance between Al sheets and steel sheets is markedly different, and at the hot leap rolling temperature of steel sheets, A
Because the l plate melted, it was produced using the cold rolling method. In this method, an Al plate and a steel plate are stacked and rolled and welded together, then diffusion heat treatment is performed, and the product is made after temper rolling. In addition, in order to obtain products with high plate thickness dimensional accuracy, diffusion heat! After 31 days, finish rolling and softening treatment are required. In the pressure rolling process of Al and steel plates, it is necessary to roll at a high rolling reduction in order to bond them to a degree that does not cause peeling, and the rolling is usually done at a rolling reduction of 30 to 70%. For this reason a
Recrystallization softening heat treatment is essential to restore the workability of the sheet. However, since Al and steel sheets easily form a brittle alloy layer when heated, the alloy layer at the interface between Al and steel sheets may peel off during processing. occurs. For this reason, a nitrogen-added rimmed steel sheet with less alloy layer formation at the recrystallization temperature is used as the core material (for example, Japanese Patent Publication No. 63-11981), and softening heat treatment is performed at the lower limit of the recrystallization field temperature. However, Al-clad steel sheets using conventional nitrogen-added rimmed steel sheets as core materials have the following problems: (1) Because the core material is rimmed steel, there are many unavoidable inclusions, and cracks occur more frequently when processed in a rough manner. (2) Because the core material is rimmed steel (ingot material), the uniformity of the material is poor due to leakage. (3) Due to the high rolling reduction rate during pressure welding, the interface between A+ and the steel plate becomes extremely uneven, resulting in N
The uniformity of the Al layer thickness is poor. (4) Because the recrystallization annealing temperature cannot be raised to a sufficiently high temperature and because a large amount of nitrogen must be added, the core material is hard. In addition, A
l When clad steel plates are manufactured, Al is added to the joint interface during heat treatment.
-The Fe alloy layer is formed and peels off during processing, making it unsatisfactory for practical use.The purpose of the present invention is to eliminate the drawbacks of the prior art described above, to improve workability, and to achieve a uniform Al shoulder thickness. Good sex A
Our goal is to provide craffoded steel sheets. (Means for Solving Problem 1) The purpose of the present invention is to use an Al quilted steel plate as a core material, which has few non-metallic inclusions, has excellent material uniformity, and has good workability. This is an Al Clathod II4 plate made by rolling and welding Al alloy plates at a rolling reduction similar to that of temper rolling. That is, the present invention provides C:0. OO1-0.1% by weight, A
The core material is an ultra-low carbon Al quilted steel plate with excellent workability, containing l+0.02~01% by weight, and the thickness ratio is 3~3.
Reduction rate of steel plate of 75% thick Al or Al alloy plate:
To provide an Al-clad steel sheet which is rolled and joined at 0.1 to 3.0%, has no alloy layer at the joint interface, has a uniform Al layer thickness, and has excellent workability. The composition of the steel plate used for this Al-clad steel plate is described below. The upper limit C is 0.1% by weight to ensure processability.
The following is preferable, and the lower limit is o. oot weight% or more. If Al is less than 0.02% by weight, deoxidation will not be sufficient and oxide-based inclusions will increase, resulting in poor workability. 0 again
．． If it exceeds 1% by weight, nitrogen in the atmosphere will be absorbed during the annealing process, resulting in increased hardness and poor workability. Therefore, the Al component should be 0.02-01% by weight. After annealing, low carbon steel sheets are usually temper rolled at a rolling reduction of 3% or less to prevent stretcher strain. When the reduction rate exceeds 3%, the workability of the steel plate deteriorates due to work hardening. In addition, the workability of the entire Al-clad steel plate is determined by the workability of the steel, which is the core material, because Al has better ductility than steel. From this, the reduction rate of pressure rolling is 3%.
It is preferable to do the following. In order to ensure the strength of the core material, rolling to 3% or more is acceptable, but workability deteriorates. In addition, when a brittle alloy layer exists at the interface between Al and the steel plate, the alloy layer at the interface between Al and the steel plate will peel off when processed.
-Al alloy layer is FeAl. FeaAls. F
eAls*, and the main phase is thought to be Fe2Als. This FetAla has a Vickers hardness of 870.
Because it is extremely hard and brittle at ~1020Hv, it is easily destroyed by processing, and the coating Al layer peels off. Furthermore, during the formation of this alloy layer, vacancies are formed at the interface between the Al layer and the alloy layer due to the Kirkendall effect due to the difference in diffusion rates between Al and Fe, resulting in bonding defects. Although it does not form even if heated for a long time, it grows in a short time when heated above the recrystallization temperature of Fe (500 to 550°C).
By plating the pot with 0 g/m2, it is possible to provide a seamless Al cladding for cans with excellent corrosion resistance, and one side has 30 to 200 mg/m2 of metal O.
r and electrolytic chromium It! which forms a 5-30 mg/m' Cr oxide layer! By applying the treatment, it is possible to provide an Al-clad steel plate for easy-open cans that has excellent corrosion resistance and an opening property equivalent to that of Al easy-open can buds. (Example) Example 1 0, 27mm thickness. 0.0511 Amount %C. 0
．． A with a pancake-type crystal structure of O6j 1% Al! The joint surfaces of the core material of the killed steel plate and the high-purity aluminum plate with a thickness of 30μ were ion-etched to a thickness of approximately 2000 angstroms in Ar gas at 5 X I O-'Torr, and then placed together at room temperature in a vacuum of 2 X 10-@Torr. In this process, the #Il plate was rolled and welded at a rolling reduction rate of 1%, and an Al-clad steel plate with an Al-killed steel core material having an Al layer thickness ratio of 10% and no Fe-Al alloy layer intervening at the interface between the Al layer and the core material was produced. It was manufactured and tested. (The presence or absence of the alloy layer was examined by polishing the cross section and using an optical 111111fi and a scanning electronic W4 microscope.As shown in the cross-section II so-called FR photograph in Figure 4, there was no intervening alloy layer. Example 2 Example After normal degreasing and pickling F! on one side of the Al-clad steel plate that has not been exposed to Al, ferrostan plating 2
In the valley 2. 8 g/m2 of silk was plated and subjected to a DI can (drawn-iron can) forming test. The core material of Al-killed #lW and the bonding surface of high-purity aluminum with a thickness of 50 μm were ion-etched to a thickness of approximately 3000 angstroms in Ar gas at 5 × 10-' Torr, overlapped, and heated at room temperature at 2 × The steel plates were rolled and welded at a rolling reduction of 3% in a vacuum of 10-' Torr. An Al-clad steel plate was manufactured using Al-killed steel with an Al thickness ratio of 20% as a core material and without an Fe-Al alloy layer interposed at the interface between the Al eyebrow and the core material. 120mg/m' of metal Cr and 15mg of Al111ipl on one side of this Al-clad steel plate
A conventional electrolytic chromic acid treatment was performed to form a Cr oxide layer of 1.2 mm/m2, and the test piece was subjected to an easy-open can forming test. Al-killed steel plate core material and plate thickness 175mm 3004
(AA symbol) 8X10-3 Torr on the aluminum alloy joint surface
Ion-etched approximately 3000 angstroms in Ar gas at
At room temperature, in a vacuum of 2x10-% Torr, both sides of the steel plate are rolled and welded at a reduction rate of 1%, and Al quilted steel is used as the core material, and an Al=Mn-Mg alloy with a thickness ratio of 70% (35+35%) is rolled and coated. Then, an Al-clad steel plate with no Fe-Al alloy layer interposed at the interface between the core material and the Al alloy was manufactured and subjected to testing. The bonding surfaces of the Al-killed steel plate core and the 60μ thick high-purity aluminum plate were ion-etched to a thickness of about 2000 angstroms in Ar gas at 5 x 10-' Torr, and then heated at room temperature to 2 x 10-' Torr. The steel plates are rolled and welded in a vacuum at a rolling reduction rate of 50% to produce an Al-clad steel plate with an Al-killed steel core material having an Al layer thickness ratio of 10% and no Fe-Al alloy layer interposed at the interface between the Al layer and the core material. The bonding surface of high-purity aluminum with a thickness of 30μ was 5×10-”T.
About 2000 angstroms of ion etching was performed in Ar gas at room temperature, 2X1 0-
'Rolling and welding the steel plates at a rolling reduction rate of 1% in a vacuum of Torr,
An Al clad steel plate is used, with a core made of rimmed steel with an Ai layer thickness ratio of 10% and no Fe-Al alloy layer interposed at the interface between the Al layer and the core, and one side that is not coated with Al is subjected to normal degreasing and degreasing. 2.8g/ in pickling treatment and ferrostane plating bath
m” tin plated, DI can (rl-iron can)
It was subjected to a molding test. The joining surface of the material and high purity aluminum with a thickness of 50μ is 5
I. Approximately 3000 angstrom ion etching was performed in Ar gas at O-'Torr. ! The steel plates were rolled and welded together at room temperature in a vacuum of 2 x 10-5 Torr at a reduction rate of 3%, using Al-killed steel with an At thickness ratio of 20% as a core material. FeAl at the interface between the Al layer and the core material
An Al-clad steel sheet without an intervening alloy layer was manufactured. 1 on one side of this Al-clad steel plate that is not A+1ffL.
20 mg/m' of metal Cr and 15 mg/m'
A conventional electrolytic chromic acid treatment was applied to form a Cr oxide layer (No. 2), and one easy-open diamond molding test was performed. The joint surfaces of the core material of the Al-quilted steel plate and the high-purity aluminum having a plate thickness of 30 μm were ion-etched to a thickness of approximately 2000 angstroms in Ar gas at 5 × 10-’ Torr, and then the joint surfaces were stacked together at room temperature at 2 × I O-’ Torr. The steel plates were rolled and welded in a vacuum at a rolling reduction of 1%, heat treated at 550°C for 5 hours, and an Al-killed steel with a thickness ratio of 81 layers of $10% was used as the core material, and the interface between the Al layer and the core material was An Al-clad steel plate with an intervening Fe-Al alloy layer was manufactured and subjected to testing. (
The presence or absence of an alloy layer was examined by polishing the cross section and using an optical lift machine and a scanning electron microscope. ) (with AI-Fe alloy layer) Surface Al of Al clad #ll plates of Example 1 and Comparative Example 1
After the layer was dissolved and removed by immersion in a 5% NaOH solution at 75°C, the surface roughness was measured using a surface roughness meter. As shown in Table 1 and Figure 1, the roughness of Example 1 is almost the same as that of the steel plate before joining, but in Ratio 11, the roughness is severe due to the high reduction ratio, and the thin part of the Al layer is rough. thick part 1
/2 or less. In this way, the thickness variation of the surface 1Il-covered Al layer is large when the reduction rate is high. The Al-clad steel plates of Example 11 and Comparative Example 2 were formed into a cup by deep drawing with the Al layer on the inner surface, and then ironed to a thickness of 250 ml so that the can wall thickness was 100 μm and the thickness of the can flange portion 2 was 160 μm. Seamless can 1 was molded into a can as shown in Figure 2. The flange of this can was widened by roll forming, and the flange was inspected for cracks. As a result, cracks were observed in 10 out of 1000 cans made using the material of Comparative Example 2, but no cracking was observed in 1000 cans made using the material of Example 2. Example 11 and Comparative Example 3. Aluminium-based steel sheets were processed into the easy-open can lid of the 202 liquid bore tie 1 shown in Figure 3 with the Al layer on the inner surface.In this processing, the rivet processing part 5 where the tab 6 is attached was processed in an ugly manner, resulting in large inclusions. If there is, cracks will occur. Cracks were observed in 6 out of 2000 diamonds made using the material of Comparative Example 3. On the other hand, no cracks were observed in the rhombus made from the material of Example 3. The cracks in the bud made with the material of Comparative Example 3 were parallel to the rolling direction of the material, and the analysis results of the cracks showed Mn. O and S are detected, and rimmed steel with many inclusions is not suitable for practical use. The Al clad #llI plates of Example 4 and Comparative Example 4 were cup-formed using a Yamada deep drawing tester. As a result, in the material of Comparative Example 4, Ill occurred at the interface between the alloy layer and the Al layer, but in the material of Example 4, no peeling was observed. [Effects of the Invention] As detailed above, according to the present invention, an aluminum alloy which combines the corrosion resistance and surface properties of Al with the excellent workability of Al quilt steel.
Since it can provide clad steel sheets, its industrial value is extremely large.
第１１３！ＩはＡｌ層除去後の芯材表面プロフィル図，
第２図はシームレス缶の断面図、第３図はイージーオー
プン缶蓋の断面図、第４図は接合部断面項微鋪写真であ
る．
１ シームレス缶、 ２： フランジ加工部、３
Ａ Ｉ 層， ４ 芯材、５．
リベット加工部 ６ タブ、
７．イージーオープン缶菱．
ルー
７。
補正の内容
４図は接合部断面の金属組織を示す顕微鏡写真である。
と訂正する。
手
続
補
正
書（方式）
平成１年特許願第５５７９７号
２，
発
明
の
名称
Ａｌクラッド鋼板
名
称
東
洋
鋼
鈑
株
式
ム
社
平成１年
５月３０日
（発送日）113th! I is the core material surface profile diagram after removing the Al layer,
Figure 2 is a cross-sectional view of a seamless can, Figure 3 is a cross-sectional view of an easy-open can lid, and Figure 4 is a close-up photograph of the joint section. 1 Seamless can, 2: Flange processing section, 3
A I layer, 4 core material, 5.
Rivet processing section 6 tabs, 7. Easy open can. Lou 7. Contents of correction Figure 4 is a micrograph showing the metal structure of a cross section of the joint. I am corrected. Procedural amendment (method) 1999 Patent Application No. 55797 2, Name of invention Al-clad steel plate Name Toyo Kohan Co., Ltd. May 30, 1999 (shipment date)
Claims (4)
〜０．１重量％を含有するＡｌキルド鋼板を芯材とし、
この芯材の少なくとも片面に厚み比率３〜７５％のＡｌ
もしくはＡｌ合金薄板が被覆層として圧接されてあり、
かつ芯材と被覆層の界面にＡｌ−ＦｅもしくはＦｅ−Ａ
ｌ系合金層が介在しないことを特徴とするＡｌクラッド
鋼板。(1) C: 0.001-0.1% by weight, Al: 0.02
An Al-killed steel plate containing ~0.1% by weight is used as a core material,
Al with a thickness ratio of 3 to 75% on at least one side of this core material.
Or an Al alloy thin plate is pressed as a covering layer,
and Al-Fe or Fe-A at the interface between the core material and the coating layer.
An Al-clad steel sheet characterized by having no intervening l-based alloy layer.
の冷間圧延接合である特許請求の範囲第１項記載のＡｌ
クラッド鋼板。(2) Pressure welding has a reduction rate of 0.1 to 3.0% in the core material.
Al according to claim 1, which is a cold-rolled joint of
Clad steel plate.
ｍ＾２の錫めっきを施された芯材である特許請求の範囲
第１項乃至第２項に記載のシームレス缶用Ａｌクラッド
鋼板。(3) The core material is 1.0 to 10.0 g/
The Al-clad steel sheet for seamless cans according to claims 1 and 2, which is a core material plated with m^2 tin.
＾２の金属Ｃｒと５〜３０ｍｇ／ｍ＾２の酸化Ｃｒ層で
なる電解クロム酸処理を施された芯材であるイージーオ
ープン缶蓋用の特許請求の範囲第１項乃至第２項に記載
のＡｌクラッド鋼板。(4) The core material is 30 to 200 mg/m on one non-bonded side.
Claims 1 and 2 describe a core material for an easy-open can lid which is a core material treated with electrolytic chromic acid, which is made of metal Cr of ^2 and Cr oxide layer of 5 to 30 mg/m^2. Al-clad steel plate.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1055797A JPH0815672B2 (en) | 1989-03-07 | 1989-03-07 | A1 clad steel plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP1055797A JPH0815672B2 (en) | 1989-03-07 | 1989-03-07 | A1 clad steel plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH02235586A true JPH02235586A (en) | 1990-09-18 |
| JPH0815672B2 JPH0815672B2 (en) | 1996-02-21 |
Family
ID=13008905
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP1055797A Expired - Fee Related JPH0815672B2 (en) | 1989-03-07 | 1989-03-07 | A1 clad steel plate |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0815672B2 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020011223A (en) * | 2000-08-01 | 2002-02-08 | 강기식 | Clad casting products and its manufacturing process |
| JP2004174894A (en) * | 2002-11-27 | 2004-06-24 | Toyo Kohan Co Ltd | Protective layer jointed body and part using the same |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58179582A (en) * | 1982-04-13 | 1983-10-20 | Nippon Steel Corp | Production of aluminum coated steel plate |
| JPS6314818A (en) * | 1986-07-05 | 1988-01-22 | Nippon Steel Corp | Steel sheet for can having excellent flanging characteristic |
| JPS6376897A (en) * | 1986-09-19 | 1988-04-07 | Nkk Corp | Electrolytically chromated steel sheet having excellent weldability and its production |
-
1989
- 1989-03-07 JP JP1055797A patent/JPH0815672B2/en not_active Expired - Fee Related
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS58179582A (en) * | 1982-04-13 | 1983-10-20 | Nippon Steel Corp | Production of aluminum coated steel plate |
| JPS6314818A (en) * | 1986-07-05 | 1988-01-22 | Nippon Steel Corp | Steel sheet for can having excellent flanging characteristic |
| JPS6376897A (en) * | 1986-09-19 | 1988-04-07 | Nkk Corp | Electrolytically chromated steel sheet having excellent weldability and its production |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20020011223A (en) * | 2000-08-01 | 2002-02-08 | 강기식 | Clad casting products and its manufacturing process |
| JP2004174894A (en) * | 2002-11-27 | 2004-06-24 | Toyo Kohan Co Ltd | Protective layer jointed body and part using the same |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0815672B2 (en) | 1996-02-21 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US5360676A (en) | Tin mill black plate for canmaking, and method of manufacturing | |
| AU761334B2 (en) | Steel band with good forming properties and method for producing same | |
| JPH0555594B2 (en) | ||
| JPH02235586A (en) | Al clad steel sheet | |
| JPS59598B2 (en) | Tampered steel plate with excellent weldability | |
| JPS61235594A (en) | Ni plated steel sheet having superior workability and corrosion resistance and its manufacture | |
| WO1995004166A1 (en) | Steel sheet of high stress-corrosion-cracking resistance for cans and method of manufacturing the same | |
| JP3017237B2 (en) | Method for producing Fe-Si-Al alloy soft magnetic thin plate | |
| JPS63499A (en) | Surface treated steel sheet for vessel | |
| JPS6311981B2 (en) | ||
| JP3239831B2 (en) | Alloyed hot-dip galvanized steel sheet and method for producing the same | |
| JP3367466B2 (en) | Galvannealed steel sheet | |
| JP2528166B2 (en) | Sn-plated ultra-thin steel sheet for cans with excellent flange formability and weldability | |
| JPH04187741A (en) | Steel sheet for can, its manufacture and manufacture of three-piece can | |
| JPH03197693A (en) | Very thin sn plated steel sheet for can and its production | |
| JP2820990B2 (en) | Surface treated steel sheet excellent in weldability and method for producing the same | |
| JP2589586B2 (en) | Manufacturing method of aluminum laminated steel sheet | |
| JPH05287488A (en) | Hot dip aluminum plated steel sheet excellent in workability and its production | |
| JPH0585619B2 (en) | ||
| JPH01172553A (en) | Alloying hot dip galvanized steel sheet and its production | |
| JP2959026B2 (en) | Ultra-thin Sn-plated steel sheet for welding can and method for producing the same | |
| JP3745457B2 (en) | Manufacturing method of steel sheet for welding can excellent in weldability, corrosion resistance, appearance and adhesion | |
| JPH08193243A (en) | Resin coated steel sheet for drawn can, free from occurrence of stretcher strain mark in can bottom, and its production | |
| JPH04105778A (en) | Production of al clad steel plate | |
| JP2023507961A (en) | Galvanized steel with excellent corrosion resistance and spot weldability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| LAPS | Cancellation because of no payment of annual fees |