JP4728114B2 - Aluminum alloy billet for heat roll production - Google Patents
Aluminum alloy billet for heat roll production Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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- G—PHYSICS
- G03—PHOTOGRAPHY; CINEMATOGRAPHY; ANALOGOUS TECHNIQUES USING WAVES OTHER THAN OPTICAL WAVES; ELECTROGRAPHY; HOLOGRAPHY
- G03G—ELECTROGRAPHY; ELECTROPHOTOGRAPHY; MAGNETOGRAPHY
- G03G15/00—Apparatus for electrographic processes using a charge pattern
- G03G15/20—Apparatus for electrographic processes using a charge pattern for fixing, e.g. by using heat
- G03G15/2003—Apparatus for electrographic processes using a charge pattern for fixing, e.g. by using heat using heat
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Description
本発明はヒートロール製造用アルミニウム合金ビレットに関し、さらに詳しくは強度、高温クリープ特性に優れ、表面が非黒色で、清浄なアルミニウム合金ビレットに関する。 The present invention relates to an aluminum alloy billet for producing heat rolls, and more particularly to a clean aluminum alloy billet that is excellent in strength and high-temperature creep characteristics, has a non-black surface, and is clean.
複写機などに使用されるヒートロールは軽量、非磁性で熱伝導性、耐熱性が要求されることからアルミニウム合金が用いられている。アルミニウム合金の中で５０５２や５０５６合金は高温強度が高い合金として知られている。そのため以前からこれらの合金がヒートロールに用いられてきている。しかしこの合金はヒートロールとして繰り返し使用されると、高温クリープ特性が十分でないので、使用中の加圧により変形することがある。またこの合金の押出加工はマンドレルを用いて行われるためコスト高となる。
上記の合金に代わるものとしてＭｎが０．５〜０．９％、Ｍｇが０．１〜２．０％含むアルミニウム合金が提案されている（特許文献１参照）。この合金はＭｎが比較的少ないので加工性は良いが強度が十分でない。特に近年は省エネの観点からヒートロールの薄肉化の傾向にあるところから、特に強度の高い合金が求められている。
Aluminum rolls are used for heat rolls used in copying machines and the like because they are lightweight, non-magnetic, heat conductive, and heat resistant. Among aluminum alloys, 5052 and 5056 alloys are known as alloys having high high-temperature strength. Therefore, these alloys have been used for heat rolls for a long time. However, when this alloy is repeatedly used as a heat roll, the high-temperature creep property is not sufficient, and may be deformed by pressurization during use. Moreover, since the extrusion process of this alloy is performed using a mandrel, the cost is increased.
As an alternative to the above alloy, an aluminum alloy containing 0.5 to 0.9% Mn and 0.1 to 2.0% Mg has been proposed (see Patent Document 1). This alloy has a relatively low Mn, so that the workability is good but the strength is not sufficient. Particularly in recent years, from the viewpoint of energy saving, there is a tendency to reduce the thickness of the heat roll, so that a particularly strong alloy is required.
またＭｎの含有量が高いヒートロール用合金としては特開平２−１４９６２８号（特許文献２）がある。この合金はＭｎが１．０〜５．０％、Ｍｇが０．１〜２．０％を含み、その他選択成分としてＺｒ、Ｃｕ、Ｎｉ、Ｓｉ、Ｃｒ、Ｚｎ、Ｆｅ、Ｔｉを少量含むものである。
上記の合金の組成範囲内でＭｇが多いものは強度は高いが、共通の問題として、合金ビレットを製造する際、Ｍｇが酸化され易く、その結果合金中に酸化物の介在物が多くなり、特性が低下するだけでなく、酸化物によりビレット表面が黒色を呈し、平滑性に劣る。ヒートロールはビレットをまず押出し、次いで引き抜き加工されて製造されるが、ビレットの表面が清浄でないと、その後の加工面に影響するするので、表面を清浄にする切削等が必要になり、加工工程が増え、コスト高となる。
In the above alloy composition range, a large amount of Mg has high strength, but as a common problem, when manufacturing an alloy billet, Mg is easily oxidized, and as a result, oxide inclusions increase in the alloy. Not only the characteristics are degraded, but the billet surface is black due to the oxide, and the smoothness is poor. The heat roll is manufactured by first extruding the billet and then drawing it, but if the billet surface is not clean, it will affect the subsequent processing surface, so it will be necessary to perform cutting etc. to clean the surface. Increases cost.
本発明は上記のような従来技術の問題点に鑑みなされたもので、強度、高温クリープ性、耐熱性に優れ、表面が黒色でなく、特にヒートロールに適したアルミニウム合金ビレットを開発することを目的とする。 The present invention has been made in view of the problems of the prior art as described above, and is to develop an aluminum alloy billet that is excellent in strength, high-temperature creep property, heat resistance, and whose surface is not black and particularly suitable for a heat roll. Objective.
本発明は上記の課題を解決するために鋭意研究した結果なされたもので、以下の各項の発明からなる。
（１）Ｍｎが０．９７〜１．５０質量％、Ｍｇが０．５０〜２．５０質量％、Ｃｕが０．２０〜１．４０質量％、Ｆｅが０．２０〜１．００質量％、Ｔｉが０．０１〜０．５０質量％、Ｂｅが０．０００１〜０．０１質量％、残部がＡｌ及び不可避的不純物であるアルミニウム合金からなるヒートロール用のビレット。
（２）Ｍｇが１．００〜２．００質量％である上記（１）に記載のビレット。
（３）Ｓｉ１．００質量％以下、Ｃｒ０．５０質量％以下、Ｚｒ０．５０質量％以下の少なくとも一種を含む上記（１）又は（２）に記載のビレット。
（４）直径が５インチ（１２．７ｃｍ）以下である上記（１）〜（３）のいずれかに記載のビレット。
（５）直径が４インチ（１０．１６ｃｍ）以下である上記（１）〜（４）のいずれかに記載のビレット。
（６）平均結晶粒径が１ｍｍ以下である上記（１）〜（５）のいずれかに記載のビレット。
（７）上記（１）〜（６）のいずれかに記載のビレットから製造されたヒートロール。
The present invention has been made as a result of intensive studies in order to solve the above problems, and comprises the inventions of the following items.
(1) Mn 0.97-1.50 mass%, Mg 0.50-2.50 mass%, Cu 0.20-1.40 mass%, Fe 0.20-1.00 mass% A billet for a heat roll comprising an aluminum alloy in which Ti is 0.01 to 0.50 mass%, Be is 0.0001 to 0.01 mass%, and the balance is Al and inevitable impurities.
(2) Billet as described in said (1) whose Mg is 1.00-2.00 mass%.
(3) Billet as described in said (1) or (2) containing at least 1 type of Si1.00 mass% or less, Cr0.50 mass% or less, Zr0.50 mass% or less.
(4) The billet according to any one of (1) to (3), wherein the diameter is 5 inches (12.7 cm) or less.
(5) The billet according to any one of (1) to (4), wherein the diameter is 4 inches (10.16 cm) or less.
(6) The billet according to any one of (1) to (5), wherein the average crystal grain size is 1 mm or less.
(7) A heat roll manufactured from the billet according to any one of (1) to (6) above.
本発明のアルミニウム合金ビレットは表面が非黒色、清浄で、その後の押し出し加工、引き抜き加工を、特に清浄化工程を設けずに行うことができ、加工工程が能率的である。
またアルミニウム合金はＢｅ添加により、Ｍｇの酸化が防止され、そのために合金中の酸化物の介在物が少なく、合金特性の劣化が防止されている。
さらに、Ｍｎ、Ｍｇの含有量が比較的高いことから、強度、高温クリープ特性、耐熱性にも優れている。Ｍｎ、Ｍｇの含有量が高いことによる加工性の問題はビレットを小さい径で鋳造し、結晶粒を抑えることにより十分に解決可能である。
The aluminum alloy billet of the present invention has a non-black surface and is clean, and the subsequent extrusion process and drawing process can be performed without particularly providing a cleaning process, and the processing process is efficient.
In addition, the addition of Be prevents the oxidation of Mg in the aluminum alloy, so that there are few oxide inclusions in the alloy and the deterioration of the alloy characteristics is prevented.
Furthermore, since the contents of Mn and Mg are relatively high, they are excellent in strength, high-temperature creep characteristics, and heat resistance. The problem of workability due to the high contents of Mn and Mg can be sufficiently solved by casting the billet with a small diameter and suppressing the crystal grains.
本発明のヒートロール用のアルミニウム合金はＭｎ、Ｍｇ、Ｃｕ、Ｆｅ、Ｔｉ、Ｂｅを必須成分として含む。
Ｍｎは合金中に０．９７〜１．５０質量％（以下％は特に断りない場合は質量％を表す）含有する。Ｍｎは、分散第二相であるＭｎＡｌ６として結晶組織内に細かく分散し、マトリックスを強化して高温クリープ特性を向上させる。Ｍｎの量は０．９７％より少ないとこの特性向上が十分でなく、また１．５０％を越えると加工性が劣り、ビレットをかなり細くしても加工が難しくなる。
The aluminum alloy for heat rolls of the present invention contains Mn, Mg, Cu, Fe, Ti, and Be as essential components.
Mn is contained in the alloy in an amount of 0.97 to 1.50 mass% (hereinafter,% represents mass% unless otherwise specified). Mn is finely dispersed in the crystal structure as MnAl 6 which is a dispersed second phase, strengthening the matrix and improving the high temperature creep characteristics. If the amount of Mn is less than 0.97%, this characteristic improvement is not sufficient, and if it exceeds 1.50%, workability is inferior, and processing becomes difficult even if the billet is made very thin.
Ｍｇはアルミニウムに固溶して存在し、合金中の強度を向上させるのに寄与する。この強度を大きくするために本発明の合金では０．５０％以上含有させる。しかしあまり多いと加工性が劣り、押出し加工が難しくなるので２．５０％が限度である。上記の範囲内で０．８０〜１．４０％が特に好ましい。
ＣｕはＡｌ−Ｃｕ−Ｍｇ系化合物を析出し、高温クリープ特性を向上させるもので、０．２０％以上必要であるが、１．４０％を越えると押出し特性が低下する。
Mg is present as a solid solution in aluminum and contributes to improving the strength in the alloy. In order to increase this strength, the alloy of the present invention contains 0.50% or more. However, if the amount is too large, the workability is inferior and the extrusion process becomes difficult, so 2.50% is the limit. Within the above range, 0.80 to 1.40% is particularly preferable.
Cu precipitates an Al—Cu—Mg compound and improves high-temperature creep characteristics. It needs to be 0.20% or more, but if it exceeds 1.40%, the extrusion characteristics deteriorate.
Ｆｅはマトリックス中にＡｌ３ＦｅとしてＭｎと共存微細析出物を形成し結晶微細化に寄与し、加工性及び高温クリープ性改善に寄与する。その効果を発現するためには０．２０％以上必要である。しかし多過ぎると粗大結晶が析出したりして特性が低下するので、１．００％以下とする。
Ｔｉは再結晶の微細化に寄与し、マトリックスを強化、加工性、高温クリープの特性を向上させる。そのために０．０１％以上必要であるが、０．５％を越えると粗大粒が発生し特性が低下する。
Fe forms coexisting fine precipitates with Mn as Al 3 Fe in the matrix and contributes to crystal refinement, and contributes to improvement of workability and high-temperature creep property. In order to exhibit the effect, 0.20% or more is necessary. However, if the amount is too large, coarse crystals will precipitate and the characteristics will deteriorate, so the content is made 1.00% or less.
Ti contributes to refinement of recrystallization, strengthens the matrix, improves workability, and high temperature creep characteristics. Therefore, 0.01% or more is necessary, but if it exceeds 0.5%, coarse particles are generated and the characteristics are deteriorated.
ＢｅはＭｇの酸化防止のために添加するものである。アルミニウム合金において、Ｍｇは酸化され易く、特にその含有量が高くなると顕著である。この酸化は主としてビレットに鋳造する際の溶湯処理の際に生じる。ＢｅはＭｇ、ＡｌよりＯ２との親和力が強く、Ｂｅの酸化膜は添加後溶湯表面を覆い、Ｍｇの酸化を防止する。その後鋳造時、鋳塊（ビレット）表面もＢｅの堅固な酸化膜で覆い、表面相の酸化を防止、表面結晶粒度粗大化防止に寄与、滑らかな表面鋳肌を形成する。Ｍｇが酸化すると、その酸化物が介在物として合金中に存在し、特性劣化の原因になるばかりでなく、ビレット表面が黒くなる。そのためにその除去等の工程が必要になる。
またＢｅはＣｕ−Ｍｇ合金晶出物の微細分散化を助け、マトリックスを強化、加工性、高温クリープ特性改善に寄与する。これらのＢｅの作用効果はＢｅの添加がわずかの場合にも生ずる。
したがってＢｅは０．０００１％以上、好ましくは０．００１％以上あればよい。その上限は、多くても作用効果が飽和するので、経済性等も考慮して０．０１％とした。
Be is added to prevent Mg oxidation. In an aluminum alloy, Mg is easily oxidized, and particularly when its content increases. This oxidation occurs mainly during the molten metal treatment when casting into billets. Be has a stronger affinity for O 2 than Mg and Al, and an oxide film of Be covers the molten metal surface after addition to prevent oxidation of Mg. After casting, the ingot (billet) surface is also covered with a solid oxide film of Be, preventing oxidation of the surface phase, contributing to prevention of coarsening of the surface crystal grain size, and forming a smooth surface casting surface. When Mg is oxidized, the oxide is present in the alloy as inclusions, causing not only deterioration of characteristics but also blackening of the billet surface. Therefore, a process such as removal is necessary.
Further, Be helps to finely disperse Cu—Mg alloy crystallized substances, and contributes to strengthening the matrix, improving workability, and improving high-temperature creep characteristics. These effects of Be occur even when a small amount of Be is added.
Therefore, Be may be 0.0001% or more, preferably 0.001% or more. The upper limit is set to 0.01% in consideration of economics and the like because the effect is saturated at most.
本発明のアルミニウム合金ビレットにはその他にＳｉ、Ｃｒ、Ｚｒが選択的に添加することができる。
ＳｉはＭｇと化合物を生成し、これが合金中に析出して 合金の強度を向上する。しかし１．００％を越えるとその化合物の析出物が粗大化するので１．００％以下が好ましい。
Ｃｒ、Ｚｒは共に再結晶粒の微細化の作用を有し、マトリックスを強化し、加工性、高温クリープ特性を向上させる。但し、０．５０％を越えると結晶が粗大化するので０．５０％以下とするのがよい。
本発明のビレットは上記の組成にした原料を溶解し、鋳造することによって得ることができる。これには冷却した円筒状の鋳型内に合金溶湯を上部より注入し、固化させ、下部より引き取る連続鋳造法が好ましい。
In addition, Si, Cr, and Zr can be selectively added to the aluminum alloy billet of the present invention.
Si forms a compound with Mg, which precipitates in the alloy and improves the strength of the alloy. However, if it exceeds 1.00%, the precipitate of the compound becomes coarse, so 1.00% or less is preferable.
Both Cr and Zr have the effect of recrystallizing grains, strengthen the matrix, and improve workability and high temperature creep characteristics. However, if it exceeds 0.50%, the crystal becomes coarse, so 0.50% or less is preferable.
The billet of the present invention can be obtained by melting and casting the raw material having the above composition. For this purpose, a continuous casting method in which molten alloy is poured into the cooled cylindrical mold from the upper part, solidified, and taken from the lower part is preferable.
本発明の合金は、その効果を高めるため急冷ホットトップ鋳造法によりビレット径は５インチ（１２．７ｃｍ）以下、望ましくは４インチ（１０．１６ｃｍ）以下のビレットに鋳造、急冷凝固、微細組織鋳塊とすることがポイントである。ビレットはその後５００〜６５０℃、好ましくは５５０〜６００℃で均質化処理する。こうして 処理されたビレットの結晶粒は通常平均１ｍｍ以下であり、さらにビレット が５インチ以下と細い場合は０．８ｍｍ以下とすることもできる。
均一化処理されたビレットは先ず４５０〜５００℃で押し出し加工を行い、次いでヒートロールの形状に冷間引き抜き加工を行う。
In order to enhance the effect, the alloy of the present invention is cast, rapidly solidified, and microstructured into billets having a billet diameter of 5 inches (12.7 cm) or less, preferably 4 inches (10.16 cm) or less by a rapid hot top casting method. The point is to make it a lump. The billet is then homogenized at 500-650 ° C, preferably 550-600 ° C. The average grain size of the billet thus treated is usually 1 mm or less, and can be 0.8 mm or less when the billet is 5 inches or less and thin.
The homogenized billet is first extruded at 450 to 500 ° C., and then cold drawn into a heat roll shape.
以下実施例により本発明を具体的に示すが本発明は実施例に限定されるものではない。
（実施例、比較例）
実施例として表１に示す組成（残部はアルミニウム及び不可避的不純物）のアルミニウム合金溶湯を連続鋳造し、直径４インチ（１０．１６ｃｍ）のビレットを製造した。表中比較例は実施例とＢｅを除きほぼ同じ組成である。
製造された各ビレットの表面状態を示す写真を図１に示す。図１の右側が実施例のもの、左側が比較例のものである。実施例のものは表面がアルミニウムの色（銀白色）であるが、比較例のものは黒色を呈している
EXAMPLES The present invention will be specifically described below with reference to examples, but the present invention is not limited to the examples.
(Examples and comparative examples)
As an example, a molten aluminum alloy having the composition shown in Table 1 (the balance being aluminum and inevitable impurities) was continuously cast to produce a billet having a diameter of 4 inches (10.16 cm). The comparative examples in the table have substantially the same composition except for the examples and Be.
The photograph which shows the surface state of each manufactured billet is shown in FIG. The right side of FIG. 1 is the example, and the left side is the comparative example. Although the thing of an Example has the surface of the color of aluminum (silver white), the thing of a comparative example is exhibiting black.
次いでビレットを５７０℃で６時間均一化処理をした。処理後のビレット断面をマクロ組織で観察した結果結晶サイズは殆ど平均１ｍｍ以下であった。 The billet was then homogenized at 570 ° C. for 6 hours. As a result of observing the billet cross section after the treatment with a macro structure, the crystal size was almost 1 mm or less on average.
本発明のアルミニウム合金はＢｅの添加により、Ｍｇの酸化が防止され、ビレットの表面が黒色にならず、その後の加工に有利である。またＢｅの添加はＣｕ−Ｍｇ合金析出物の微細分散化を助け、マトリックスを強化、加工性、高温クリープ特性を改善する。その結果、ヒートロール製造用の優れた合金として産業上の利用性が高い。 The addition of Be prevents the oxidation of Mg in the aluminum alloy of the present invention, and the billet surface does not become black, which is advantageous for subsequent processing. Also, the addition of Be helps to finely disperse Cu—Mg alloy precipitates, strengthens the matrix, improves workability, and high temperature creep characteristics. As a result, industrial applicability is high as an excellent alloy for manufacturing heat rolls.
Claims (7)
The heat roll manufactured from the billet in any one of Claims 1-6.
Priority Applications (4)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005357239A JP4728114B2 (en) | 2005-12-12 | 2005-12-12 | Aluminum alloy billet for heat roll production |
| TW095146288A TW200732481A (en) | 2005-12-12 | 2006-12-11 | Alluminum alloy billet for heat roll, and heat roll |
| CNB2006101656865A CN100510135C (en) | 2005-12-12 | 2006-12-12 | Aluminum alloy billet for heat roll, and heat roll |
| KR1020060126146A KR20070062442A (en) | 2005-12-12 | 2006-12-12 | Aluminum Alloy Billet and Heatrol |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005357239A JP4728114B2 (en) | 2005-12-12 | 2005-12-12 | Aluminum alloy billet for heat roll production |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2007162046A JP2007162046A (en) | 2007-06-28 |
| JP4728114B2 true JP4728114B2 (en) | 2011-07-20 |
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| JP2005357239A Expired - Fee Related JP4728114B2 (en) | 2005-12-12 | 2005-12-12 | Aluminum alloy billet for heat roll production |
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|---|---|
| JP (1) | JP4728114B2 (en) |
| KR (1) | KR20070062442A (en) |
| CN (1) | CN100510135C (en) |
| TW (1) | TW200732481A (en) |
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| US8093806B2 (en) | 2007-06-20 | 2012-01-10 | Semiconductor Energy Laboratory Co., Ltd. | Light-emitting device, method for manufacturing the same, and electronic apparatus |
| CN103725939A (en) * | 2013-12-17 | 2014-04-16 | 芜湖万润机械有限责任公司 | Preparation method of aluminium alloy section for hot roller of duplicator |
| CN111733467A (en) * | 2020-07-16 | 2020-10-02 | 无锡中力科技有限公司 | High-speed rotating aluminum alloy hot roller and processing method thereof |
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| JPS62133038A (en) * | 1985-12-04 | 1987-06-16 | Showa Alum Corp | Aluminum alloy with excellent mirror machinability |
| JPH02149628A (en) * | 1988-11-30 | 1990-06-08 | Showa Alum Corp | Aluminum alloy for heat roller |
| JPH0328342A (en) * | 1989-06-23 | 1991-02-06 | Kobe Steel Ltd | Aluminum alloy having excellent extrudability and cold workability |
| JPH09125182A (en) * | 1995-11-01 | 1997-05-13 | Samitsuto Alum Kk | Aluminum alloy for casting high in elongation |
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| Publication number | Publication date |
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| KR20070062442A (en) | 2007-06-15 |
| TW200732481A (en) | 2007-09-01 |
| CN100510135C (en) | 2009-07-08 |
| JP2007162046A (en) | 2007-06-28 |
| CN1982487A (en) | 2007-06-20 |
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