EP1676931A2 - Aluminium-Legierung für lithographische Platte - Google Patents

Aluminium-Legierung für lithographische Platte Download PDF

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Publication number
EP1676931A2
EP1676931A2 EP06075572A EP06075572A EP1676931A2 EP 1676931 A2 EP1676931 A2 EP 1676931A2 EP 06075572 A EP06075572 A EP 06075572A EP 06075572 A EP06075572 A EP 06075572A EP 1676931 A2 EP1676931 A2 EP 1676931A2
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EP
European Patent Office
Prior art keywords
present
lithographic sheet
alloy
amount
sheet according
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.)
Withdrawn
Application number
EP06075572A
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English (en)
French (fr)
Other versions
EP1676931A3 (de
Inventor
Theodor Rottwinkel
David Skingley Wright
Richard Gary Hamerton
Jeremy Mark Brown
John Andrew Ward
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Novelis Inc Canada
Original Assignee
Novelis Inc Canada
Priority date (The priority date 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 date listed.)
Filing date
Publication date
Priority claimed from GB0118100A external-priority patent/GB0118100D0/en
Application filed by Novelis Inc Canada filed Critical Novelis Inc Canada
Priority to EP06075572A priority Critical patent/EP1676931A3/de
Publication of EP1676931A2 publication Critical patent/EP1676931A2/de
Publication of EP1676931A3 publication Critical patent/EP1676931A3/de
Withdrawn legal-status Critical Current

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Classifications

    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B41—PRINTING; LINING MACHINES; TYPEWRITERS; STAMPS
    • B41N—PRINTING PLATES OR FOILS; MATERIALS FOR SURFACES USED IN PRINTING MACHINES FOR PRINTING, INKING, DAMPING, OR THE LIKE; PREPARING SUCH SURFACES FOR USE AND CONSERVING THEM
    • B41N1/00—Printing plates or foils; Materials therefor
    • B41N1/04—Printing plates or foils; Materials therefor metallic
    • B41N1/08—Printing plates or foils; Materials therefor metallic for lithographic printing
    • B41N1/083—Printing plates or foils; Materials therefor metallic for lithographic printing made of aluminium or aluminium alloys or having such surface layers
    • 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
    • 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
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent

Definitions

  • This invention relates to an Al alloy suitable for processing into a lithographic sheet, which exhibits good mechanical properties with good electrograining characteristics.
  • the lithographic sheet market largely consists of products in the 1XXX and 3XXX alloy range.
  • the 1XXX alloys are used with both nitric and hydrochloric acid electrolytes and generally have the better graining response.
  • the 3XXX alloys mainly AA3103, are used where greater strength is demanded by the printer but can only be grained in hydrochloric acid, and even then not by all platemakers.
  • an Al alloy suitable for processing into a lithographic sheet having a composition in wt%: Mg 0.05 to 0.30 Mn 0.05 to 0.25 Fe 0.11 to 0.40 Si up to 0.25 Ti up to 0.03 B up to 0.01 Cu up to 0.01 Cr up to 0.03 Zn up to 0.15
  • the alloy is relatively cheap to produce as it contains alloying elements in smaller amounts compared with AA3103. Furthermore, the alloy has an added commercial benefit by providing the potential for reduced inventories for manufacturers and their customers. The alloy has also been found to resist the softening encountered during stoving or heating at temperatures of about 240°C or even 270°C.
  • magnesium and manganese are sufficient to attain much improved mechanical properties while still allowing adequate electrograining in hydrochloric acid, and preferably in nitric acid in some embodiments.
  • Magnesium is preferably present in an amount of 0.06 to 0.30wt%, even more preferably 0.10 to 0.30-wt%. Magnesium is the element influencing work hardening in the alloy. However, if the magnesium level is raised too far, then electrograining becomes increasingly difficult especially in nitric acid electrolyte.
  • Manganese is present in an amount of 0.05 to 0.25wt%, preferably in an amount of 0.05 to 0.20wt%. In either case, the lower limit of Mn may optionally be 0.06wt%. Manganese provides maximum stoved strength, and a minimum drop in strength compared with the as cold rolled sheet. The optimum upper level of manganese is determined by a balance between the desirable stoving resistance on the one hand and the onset of an undesirable level of streaking and discolouration after electrograining on the other hand.
  • copper is present in an amount up to 0.005%, more preferably up to 0.003%.
  • Ti is present in total amounts of up to 0.03wt%.
  • up to 0.028wt% of the titanium is free i.e. present in solid solution and not tied up for example as the boride, TiB 2 .
  • titanium is present in a total amount up to 0.015 wt%, even more preferably 0.010 wt%.
  • Grain refiner may or may not be present; if it is, some additional titanium is present over that found in virgin metal. It has been found that if the free titanium content is too high, this may have a detrimental effect on the ability to grain the formed lithographic sheet in nitric acid, although it may still be grainable in hydrochloric acid.
  • the level of titanium preferably needs to be controlled. If too much free titanium is present it is detrimental to graining; titanium combined with boron is not detrimental.
  • B is preferably present in an amount up to 0.002.
  • zinc may be present in an amount of up to 0.05wt%.
  • a zinc content in the range of 0.01 to 0.15wt% has been found to be advantageous in order that the alloy can be satisfactorily grained by electrograining in nitric acid.
  • the zinc content of the alloy will typically be in the range of from 0.01 to 0.1wt% and more preferably from about 0.01 to 0.08wt%.
  • Especially preferred zinc contents will be in the range of from 0.015 to 0.06wt% and most preferably from about 0.02 to about 0.05wt%.
  • Zirconium may typically be present in amounts up to 0.019wt%, for example up to 0.015wt%, particularly up to 0.005wt%. In a preferred embodiment, there is no deliberate addition of zirconium.
  • iron is present in an amount of 0.20 to 0.40%.
  • Silicon may be present in an amount of 0.05 to 0.15%, for example 0.09 to 0.15%.
  • Such alloys have been found to exhibit good strength properties in both the as-rolled and stoved embodiments, and are reasonably cost effective for use in high volume production of lithographic sheet.
  • Silicon in solution alters the reactivity of the sheet during electrograining. If the amount of silicon present is too small, too many pits form during graining and the surface is not suitable for lithographic sheet. If the amount of silicon present is too great, too few pits form during electrograining and they are too large.
  • Iron in solution has a similar effect to silicon as regards electrograining.
  • iron forms intermetallic phases present as particles in the sheet. The presence of too many of these iron containing particles is detrimental to graining.
  • a lithographic sheet formed from the alloy in such a lithographic sheet, titanium may be present in an amount sufficient to enable the sheet to be capable of being electrograined in nitric acid, although it should be borne in mind that in some embodiments of the invention the presence of titanium is not essential to the ability to electrograin in nitric acid.
  • free Ti is present up to 0.028wt% in general but only up to 0.019wt%, for example up to 0.015wt%, for nitric acid graining.
  • TiB 2 is, in one embodiment, present up to 170ppm, but it can be higher.
  • a DC cast ingot comprising the alloy.
  • a method of processing an Al alloy as defined above comprises the steps of: casting, optional homogenising, optional hot rolling, cold rolling, optional interannealing.
  • the casting step is, in one embodiment, a DC casting step.
  • the DC cast ingots are scalped prior to the homogenising step. Homogenising is used to get the right amount of Fe and Mn in solid solution. Other casting options include roll casting or belt casting. If these continuous casting processes are used, then homogenising and scalping may not be necessary. This is because the rapid cooling in continuous casting holds a lot of Fe and Mn in solid solution.
  • Heat treatment after casting and before hot rolling affects both the strength loss during stoving and the response to electrograining. To some extent the effects are contradictory and an optimum treatment has to be found.
  • Two alternative homogenising treatments are envisaged. Firstly, there is a two stage homogenisation designated Type 2. This involves slow heating of the alloy to a temperature higher than the rolling temperature and holding at this temperature. During heating to this temperature and during holding, Mn is taken into solution. The ingot is then cooled to the hot rolling temperature and rolled either after holding for a period or immediately on reaching the hot rolling temperature. Some Mn will come out of solution during cooling but the process is slow and most will remain in supersaturated solution.
  • An example of this treatment is: slow heat to 550 to 610°C and holding in that temperature range for typically 1 to 10 hours. This is followed by cooling to the rolling temperature and hot rolling at a temperature of between 450 to 550°C.
  • the homogenisation may be carried out with a heat-to-roll practice (designated Type 1). This involves heating the alloy as cast (and scalped) to the hot rolling temperature, typically 450 to 550°C, by ramped heating and holding at that temperature for 1 to 16 hours prior to hot rolling. This treatment consumes less energy and take less time than the Type 2 treatment and is therefore less expensive.
  • Type 1 treatment minimises the amount of Mn taken into solution. This benefits electrograining but the strength loss during subsequent stoving is greater. Variations or combinations of these two treatments may be required to achieve the optimum combination of strength after stoving and good electrograining response.
  • an intermediate annealing step it may be carried out immediately after hot rolling or during cold rolling.
  • the interannealing may be carried out as batch interannealing, in which case it is preferably carried out at 300 to 500°C, for example for 1 to 5 hours.
  • the interannealing may be continuous, in which case it is preferably carried out at 450 to 600°C, preferably for less than 10 minutes, for example for up to 5 minutes, even more preferably up to 1 minute.
  • at least forced air quenching is used. It is preferred to cool rapidly in order to hold Mn and Fe in solid solution.
  • the cold roll reduction of the sheet thickness is greater than 30%, preferably greater than 50%.
  • An electrograining step may also be provided.
  • the alloy is capable of being electrograined in hydrochloric acid, even more preferably in both hydrochloric and nitric acids.
  • Further steps which may be provided are anodising and stoving. Stoving trials are typically carried out at 240°C for 10 minutes or even 270°C for 10 minutes to harden the photosensitive coating prior to printing.
  • stoving is simulated by heating the plate to 240°C for 10 minutes or, where noted, to 270°C for 10 minutes.
  • Printers use less time than 10 minutes, typically 3 minutes in continuous ovens, up to 7 minutes in others, and therefore the simulated stoving is a particularly severe test because the degree of softening increases with both time and temperature of stoving.
  • the plate softens via the mechanisms of recovery and recrystallisation of the microstructure and the inherent anisotropy in the plate can lead to off-flatness problems. As mentioned above, the present invention minimises such problems. Generally, as low a drop in proof strength as possible is required.
  • a method of forming a lithographic sheet comprising electrograining an aluminium metal sheet formed of the above-mentioned alloy in a nitric acid electrolyte until a total charge input of above 82kC/m 2 is applied, wherein the surface of the lithographic sheet comprises a pitted structure.
  • the total charge input is about 87kC/m 2 .
  • the pitted structure may provide total coverage of the surface of the material and sufficient roughness to allow good adhesion of a light-sensitive coating, together with good wear resistance and water retention following anodising and post anodic treatment.
  • compositions given in Table 1 are rounded to the nearest significant figure and Std means typical AA1050A with the compositions shown.
  • Rolling blocks approximately 70mm thick by 180mm wide by 200mm long were scalped from ingots cast in large book moulds.
  • the rolling blocks were homogenised by heating slowly to 600°C and holding for several hours followed by a 2 hour cool to 500°C for 10 hours to allow equilibration of solute to occur, prior to hot rolling.
  • This two-stage homogenisation is an example of a Type 2 pre-heat.
  • the rolling blocks were hot rolled to an intermediate gauge of about 9mm with a finish temperature of about 150°C and allowed to air cool. Subsequent cold rolling to a final gauge of 0.3mm was done with an intermediate anneal at about 2mm gauge by heating to 450°C and holding for 2 hours.
  • the tensile properties of the final gauge sheet, before and after a simulated stoving treatment for 10 minutes at 240°C, were measured in the longitudinal and transverse orientations (with respect to the rolling direction).
  • Figures 1 a and 1b show, respectively, the proof strength and tensile strength at final gauge in the as rolled (H18) condition and after stoving for the Mn and Mg additions. It can be seen that even small Mg additions give significant work hardening effect and thus a higher as rolled strength. However on stoving the drop in strength is also large. The maximum stoved strength (and minimum drop in strength) is seen in the Mn containing alloys.
  • compositions given in Table 2 are rounded to the nearest significant figure and Std means typical AA1050A with the additions shown.
  • Rolling blocks were manufactured in a similar manner to that described in Example 1.
  • a set of blocks were homogenised with a heat-to-roll practice (Type 1). This consists of a ramped heating to the rolling temperature of 500°C and holding for a few hours (total heating cycle about 16 hours).
  • the blocks were either rolled to final gauge with an interanneal, as above, to give material in the H18 condition, or without any interanneal to give material in the H19 condition.
  • the H19 route is more economical while the H18 route gives an opportunity to control solute and grain structure, and hence stoving response and surface streakiness in the final gauge product.
  • Figures 4a to 4d illustrate property-electrograining maps for homogenising treatments Type 1 and Type 2 in the H18 or H19 condition.
  • Figures 4a and 4b show graining and proof strength results after stoving for 10 minutes at 240°C for Type 1 and Type 2 homogenisation respectively in H18 conditions.
  • Figures 4c and 4d show similar results for Type 1 and 2 homogenisation respectively in the H19 condition. There is sufficient overlap between the good strength properties and the good graining response in the alloy range tested.
  • Ti is an important element in electrograining response in nitric acid. So a middle level Mn/Mg variant was chosen and ingots were cast with a range of Ti levels, as shown in Table 4 and heat treated and rolled as in Example 2: TABLE 4.
  • Ti Unialloy Variants Wt% Mg Wt% Mn Wt% B Wt% Ti (total) Wt% free Ti* 0.10 0.10 0.0011 0.010 0.008 0.10 0.10 0.0011 0.013 0.011 0.10 0.10 0.0012 0.018 0.015 0.10 0.10 0.0011 0.021 0.019 Cu, Cr and Zr all 0.001 wt% for all variants shown in Table 4. *Ti in the Al solid solution and not including Ti combined with B as TiB 2 particles.
  • Figure 8 shows that the final gauge stoving response of the alloy labelled 1 st version in Table 6 is independent of the interannealing temperature compared to the AA1050A alloy. This is consistent with the stoving resistance being controlled by manganese in solid solution, which has a high solid solubility over this temperature range. Fe has a very low solubility resulting in a high driving force for Fe precipitation during inter-anneal. Consequently a high interannealing temperature is usually used to keep Fe solute levels high in the AA1050A product.
  • An advantage of the new alloy is that it could be supplied in the H18 condition for intermediate strength applications by using a relatively low inter-anneal temperature thus saving production costs.
  • the blocks were either rolled to final gauge with an interanneal, as above, to give material in the H18 condition, or without interanneal to give material in the H19 condition. Stoving was carried out for 10 minutes at various temperatures to simulate the actions of a printer and the results are shown in Figures 9a - c. From this it can be seen that material in the H19 condition for the alloys shown has a higher strength than in the H18 condition. At higher baking temperatures the material containing Mn in the H19 condition has much better mechanical properties than the comparison material in a similar condition.
  • compositions I, II and III were prepared using a Type 2 homogenisation and were electrograined as described in Example 3 with the exception that the voltage applied was lower than standard, in order to demonstrate the sensitivity.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Printing Plates And Materials Therefor (AREA)
  • Conductive Materials (AREA)
  • Chemical Treatment Of Metals (AREA)
  • Continuous Casting (AREA)
  • ing And Chemical Polishing (AREA)
EP06075572A 2000-12-11 2001-12-11 Aluminium-Legierung für lithographische Platte Withdrawn EP1676931A3 (de)

Priority Applications (1)

Application Number Priority Date Filing Date Title
EP06075572A EP1676931A3 (de) 2000-12-11 2001-12-11 Aluminium-Legierung für lithographische Platte

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
EP00311029 2000-12-11
GB0118100A GB0118100D0 (en) 2001-07-25 2001-07-25 A1 alloy for lithographic sheet
EP01270197A EP1341942B1 (de) 2000-12-11 2001-12-11 Aluminiumlegierung für lithographische druckplatte
EP06075572A EP1676931A3 (de) 2000-12-11 2001-12-11 Aluminium-Legierung für lithographische Platte

Related Parent Applications (1)

Application Number Title Priority Date Filing Date
EP01270197A Division EP1341942B1 (de) 2000-12-11 2001-12-11 Aluminiumlegierung für lithographische druckplatte

Publications (2)

Publication Number Publication Date
EP1676931A2 true EP1676931A2 (de) 2006-07-05
EP1676931A3 EP1676931A3 (de) 2006-07-26

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EP06075572A Withdrawn EP1676931A3 (de) 2000-12-11 2001-12-11 Aluminium-Legierung für lithographische Platte
EP01270197A Expired - Lifetime EP1341942B1 (de) 2000-12-11 2001-12-11 Aluminiumlegierung für lithographische druckplatte

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US (3) US20040047759A1 (de)
EP (2) EP1676931A3 (de)
JP (1) JP4107489B2 (de)
AT (1) ATE320513T1 (de)
AU (1) AU2002222144A1 (de)
DE (1) DE60117916T2 (de)
ES (1) ES2259311T3 (de)
WO (1) WO2002048415A1 (de)

Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009068502A1 (de) * 2007-11-30 2009-06-04 Hydro Aluminium Deutschland Gmbh Aluminiumband für lithografische druckplattenträger und dessen herstellung
EP2243849A1 (de) 2009-04-24 2010-10-27 Hydro Aluminium Deutschland GmbH Mangan- und hoch magnesiumreiches Aluminiumband
RU2522242C2 (ru) * 2009-04-24 2014-07-10 Гидро Алюминиум Дойчланд Гмбх Алюминиевая лента с высоким содержанием марганца и магния

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JP4318587B2 (ja) * 2003-05-30 2009-08-26 住友軽金属工業株式会社 平版印刷版用アルミニウム合金板
JP4161134B2 (ja) * 2004-06-25 2008-10-08 日本軽金属株式会社 印刷版用アルミニウム合金素板の製造方法
WO2006134542A2 (en) * 2005-06-15 2006-12-21 Hulett Aluminium (Proprietary) Limited Aluminium alloy for lithographic sheet and process for producing the same
ES2435404T5 (es) 2005-10-19 2021-02-22 Hydro Aluminium Rolled Prod Procedimiento para la fabricación de una banda de aluminio para soportes de planchas de impresión litográficos
ES2524005T5 (es) 2006-02-13 2018-12-10 Hydro Aluminium Rolled Products Gmbh Aleación de aluminio libre de carburo de aluminio
EP2077949B1 (de) * 2006-03-31 2015-09-30 Aludium Transformación de Productos, S.L.U. Fertigungsverfahren zur herstellung einer lithographischen druckplatte
US20110039121A1 (en) * 2007-11-30 2011-02-17 Hydro Aluminium Deutschland Gmbh Aluminum strip for lithographic printing plate carriers and the production thereof
WO2009144108A1 (en) * 2008-05-28 2009-12-03 Novelis Inc. Composite aluminium lithographic sheet
GB2461240A (en) * 2008-06-24 2009-12-30 Bridgnorth Aluminium Ltd Aluminium alloy for lithographic sheet
ES2501595T3 (es) * 2009-05-08 2014-10-02 Novelis, Inc. Plancha litográfica de aluminio
DE102010031468A1 (de) * 2010-07-16 2012-01-19 Behr Gmbh & Co. Kg Fluidkanal für einen Wärmetauscher
JP2012072487A (ja) * 2010-09-03 2012-04-12 Fujifilm Corp 平版印刷版用アルミニウム合金板及びその製造方法
WO2012059362A1 (en) 2010-11-04 2012-05-10 Novelis Inc. Aluminium lithographic sheet
CN104264001B (zh) * 2014-09-16 2016-08-17 广东新劲刚新材料科技股份有限公司 一种原位自生颗粒增强的铝基复合材料及其制备方法
RU2639284C2 (ru) * 2015-03-20 2017-12-20 Общество с ограниченной ответственностью "СЕВАН" Термокоррозионно-стойкий алюминиевый сплав
JP6629992B2 (ja) * 2016-04-20 2020-01-15 ハイドロ アルミニウム ロールド プロダクツ ゲゼルシャフト ミット ベシュレンクテル ハフツングＨｙｄｒｏ Ａｌｕｍｉｎｉｕｍ Ｒｏｌｌｅｄ Ｐｒｏｄｕｃｔｓ ＧｍｂＨ 高率の冷間圧延パス短縮によるリソ・ストリップの製造方法
WO2018044835A2 (en) 2016-09-01 2018-03-08 Novelis Inc. Aluminum-manganese-zinc alloy
CN110373577B (zh) * 2019-08-29 2020-08-07 国网河北能源技术服务有限公司 一种亚微米TiB2复合铝导线及其制备方法
CN112853160A (zh) * 2020-12-31 2021-05-28 蔚然（南京）动力科技有限公司 一种电机转子铸造铝合金及其制备方法

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EP0097318A2 (de) * 1982-06-18 1984-01-04 Furukawa Aluminum Co., Ltd. Aluminiumbogen für Offsetflachdruck
JPS6286143A (ja) * 1985-10-11 1987-04-20 Sky Alum Co Ltd 印刷版支持体用アルミニウム合金素板
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Publication number Priority date Publication date Assignee Title
EP0097318A2 (de) * 1982-06-18 1984-01-04 Furukawa Aluminum Co., Ltd. Aluminiumbogen für Offsetflachdruck
JPS6286143A (ja) * 1985-10-11 1987-04-20 Sky Alum Co Ltd 印刷版支持体用アルミニウム合金素板
US4822715A (en) * 1986-04-01 1989-04-18 Furukawa Aluminum Co., Ltd. Aluminum alloy supporter for lithographic printing plate
US5372780A (en) * 1989-11-22 1994-12-13 Alcan International Limited Aluminum alloys suitable for lithographic printing plates
JPH05263172A (ja) * 1992-03-17 1993-10-12 Furukawa Alum Co Ltd 熱交換器フィン材用アルミニウム合金
EP1065071A1 (de) * 1999-07-02 2001-01-03 VAW aluminium AG Lithoband und Verfahren zu seiner Herstellung

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
WO2009068502A1 (de) * 2007-11-30 2009-06-04 Hydro Aluminium Deutschland Gmbh Aluminiumband für lithografische druckplattenträger und dessen herstellung
EP2067871A1 (de) * 2007-11-30 2009-06-10 Hydro Aluminium Deutschland GmbH Aluminiumband für lithografische Druckplattenträger und dessen Herstellung
US11326232B2 (en) 2007-11-30 2022-05-10 Hydro Aluminium Deutschland Gmbh Aluminum strip for lithographic printing plate carriers and the production thereof
EP2243849A1 (de) 2009-04-24 2010-10-27 Hydro Aluminium Deutschland GmbH Mangan- und hoch magnesiumreiches Aluminiumband
WO2010122144A1 (de) * 2009-04-24 2010-10-28 Hydro Aluminium Deutschland Gmbh Mangan- und hoch magnesiumreiches aluminiumband
RU2522242C2 (ru) * 2009-04-24 2014-07-10 Гидро Алюминиум Дойчланд Гмбх Алюминиевая лента с высоким содержанием марганца и магния

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ES2259311T3 (es) 2006-10-01
EP1341942A1 (de) 2003-09-10
WO2002048415A1 (en) 2002-06-20
JP4107489B2 (ja) 2008-06-25
JP2004515652A (ja) 2004-05-27
AU2002222144A1 (en) 2002-06-24
DE60117916D1 (de) 2006-05-11
DE60117916T2 (de) 2006-11-16
US20040047759A1 (en) 2004-03-11
US20060254680A1 (en) 2006-11-16
EP1341942B1 (de) 2006-03-15
US20110056595A1 (en) 2011-03-10
ATE320513T1 (de) 2006-04-15
EP1676931A3 (de) 2006-07-26

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