EP2138592A2 - Alloy - Google Patents
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- Publication number
- EP2138592A2 EP2138592A2 EP09251641A EP09251641A EP2138592A2 EP 2138592 A2 EP2138592 A2 EP 2138592A2 EP 09251641 A EP09251641 A EP 09251641A EP 09251641 A EP09251641 A EP 09251641A EP 2138592 A2 EP2138592 A2 EP 2138592A2
- Authority
- EP
- European Patent Office
- Prior art keywords
- alloy
- electrograining
- aluminium
- strength
- bend
- 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.)
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- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 106
- 239000000956 alloy Substances 0.000 title claims abstract description 106
- 229910000838 Al alloy Inorganic materials 0.000 claims abstract description 12
- 238000012545 processing Methods 0.000 claims abstract description 9
- 239000000203 mixture Substances 0.000 claims abstract description 8
- 229910052782 aluminium Inorganic materials 0.000 claims description 31
- 239000004411 aluminium Substances 0.000 claims description 30
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 30
- 238000000034 method Methods 0.000 claims description 21
- 239000011572 manganese Substances 0.000 claims description 19
- 239000011777 magnesium Substances 0.000 claims description 17
- 229910052749 magnesium Inorganic materials 0.000 claims description 13
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims description 12
- 229910052748 manganese Inorganic materials 0.000 claims description 12
- 239000011701 zinc Substances 0.000 claims description 12
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims description 11
- 239000010949 copper Substances 0.000 claims description 9
- 229910052725 zinc Inorganic materials 0.000 claims description 7
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 6
- JBQYATWDVHIOAR-UHFFFAOYSA-N tellanylidenegermanium Chemical compound [Te]=[Ge] JBQYATWDVHIOAR-UHFFFAOYSA-N 0.000 claims 1
- 238000012360 testing method Methods 0.000 description 22
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 19
- 239000000463 material Substances 0.000 description 14
- VEXZGXHMUGYJMC-UHFFFAOYSA-N Hydrochloric acid Chemical compound Cl VEXZGXHMUGYJMC-UHFFFAOYSA-N 0.000 description 12
- 239000011248 coating agent Substances 0.000 description 10
- 238000000576 coating method Methods 0.000 description 10
- 239000003792 electrolyte Substances 0.000 description 9
- 229910052742 iron Inorganic materials 0.000 description 9
- 239000010936 titanium Substances 0.000 description 8
- 238000004519 manufacturing process Methods 0.000 description 7
- 238000001000 micrograph Methods 0.000 description 7
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical compound O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 6
- 229910017604 nitric acid Inorganic materials 0.000 description 6
- 238000007639 printing Methods 0.000 description 6
- 230000002411 adverse Effects 0.000 description 5
- 229910052802 copper Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000005096 rolling process Methods 0.000 description 5
- 238000007788 roughening Methods 0.000 description 5
- 229910052719 titanium Inorganic materials 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 4
- 230000008901 benefit Effects 0.000 description 4
- 238000005266 casting Methods 0.000 description 4
- 229910052751 metal Inorganic materials 0.000 description 4
- 239000002184 metal Substances 0.000 description 4
- 238000004064 recycling Methods 0.000 description 4
- 230000000977 initiatory effect Effects 0.000 description 3
- 239000000243 solution Substances 0.000 description 3
- 238000007792 addition Methods 0.000 description 2
- 238000005452 bending Methods 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000006866 deterioration Effects 0.000 description 2
- 238000010438 heat treatment Methods 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 230000000670 limiting effect Effects 0.000 description 2
- 238000005259 measurement Methods 0.000 description 2
- 238000007645 offset printing Methods 0.000 description 2
- 238000004439 roughness measurement Methods 0.000 description 2
- 230000003068 static effect Effects 0.000 description 2
- 239000000758 substrate Substances 0.000 description 2
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 2
- 239000012670 alkaline solution Substances 0.000 description 1
- WNROFYMDJYEPJX-UHFFFAOYSA-K aluminium hydroxide Chemical compound [OH-].[OH-].[OH-].[Al+3] WNROFYMDJYEPJX-UHFFFAOYSA-K 0.000 description 1
- 229910021502 aluminium hydroxide Inorganic materials 0.000 description 1
- 238000004458 analytical method Methods 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 239000010407 anodic oxide Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000001680 brushing effect Effects 0.000 description 1
- 230000003749 cleanliness Effects 0.000 description 1
- 238000005097 cold rolling Methods 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000001627 detrimental effect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000004090 dissolution Methods 0.000 description 1
- 238000003487 electrochemical reaction Methods 0.000 description 1
- 238000005530 etching Methods 0.000 description 1
- 230000001747 exhibiting effect Effects 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000005098 hot rolling Methods 0.000 description 1
- 230000014759 maintenance of location Effects 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 238000000399 optical microscopy Methods 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 230000000171 quenching effect Effects 0.000 description 1
- 230000002829 reductive effect Effects 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 230000003746 surface roughness Effects 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 238000012876 topography Methods 0.000 description 1
- 238000011282 treatment Methods 0.000 description 1
- 238000009827 uniform distribution Methods 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
Images
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
- 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
Definitions
- This invention relates to an alloy suitable for processing into a lithographic sheet, to an alloy in the form of a thin rolled aluminium strip particularly for use by offset printing plate makers and to a method of processing such a lithographic sheet.
- aluminium alloy in the form of a thin rolled aluminium strip is used by offset printing plate makers.
- plate makers will initially degrease or etch the aluminium strip, typically in an alkaline solution. This process prepares the surface of the aluminium for graining, and evens out minor surface imperfections.
- Electrograining is then carried out to create a surface topography with convoluted hemispherical pits. This is typically carried out in an electrolyte based on hydrochloric acid, or in one based on nitric acid.
- Electrograining is carried out using an alternating current (AC) through an electrolytic cell containing the aluminium strip.
- AC alternating current
- the electro-chemical reactions that take place on each half cycle effectively remove aluminium from the surface by dissolution.
- the surface of the aluminium strip may be mechanically roughened, for example by brushing. This process is, however, less common.
- the function of the pits formed in the surface of the aluminium strip is to increase the surface area of the aluminium strip, and to hold water. In other words, due to the presence of the pits, the aluminium strip becomes hydrophilic.
- a desmutting step may then be carried out in order to remove aluminium hydroxide smut created during the electrograining process.
- the aluminium strip is anodised. This results in the growth of a porous anodic oxide on the pitted surface of the aluminium strip.
- This provides a hard wearing coating which enhances the longevity of print quality of a lithographic sheet formed from the aluminium strip. It also enables better adhesion of the light-sensitive coating and makes the plate more chemically inert, thus improving its sheff-life.
- a photosensitive polymeric coating is then applied to the aluminium strip. This coating repels water, but attracts oil. It is required that the lithographic sheet attracts oil, since printing ink is oil-based.
- the lithographic plate comprises a hydrophilic anodised aluminium layer covered by an oleophilic photosensitive layer.
- an image is created by removing parts of the coating, for example by exposure to light.
- the coating must also be hard-wearing in order to retain a well defined image during printing runs.
- the aluminium strip used to form the lithographic sheet has sufficient strength and appropriate surface functionality.
- surface functionality is used to describe the ability of a material to electrograin well in order to provide a uniform distribution in size of pits without any surface streakiness or directionality being formed. This is important for the quality of the resulting printed images.
- the first alloy type is known as AA1050 and has the composition set out in Table 1 below. AA1050 exhibits good electrograining behaviour.
- a material has "good electrograining behaviour" it means that the material has the ability to produce a uniformly pitted surface under a broad range of conditions. Such a material should also be capable of electrograining in either hydrochloric acid or nitric acid based electrolytes.
- Table 1 Alloy Fe% Si% Cu% Mn% Mg% Zn% Ti% V% Others % Al% AA1050 Up to 0.40 Up to 0.25 Up to 0.05 Up to 0.05 Up to 0.05 Up to 0.03 Up to 0.05 Up to 0.03 99.50 min AA1050A Up to 0.40 Up to 0.25 Up to 0.05 Up to 0.05 Up to 0.07 Up to 0.05 Not defined Up to 0.03 99.50 min
- a second alloy type is known as AA3XXX and comprises AA3103 or AA3003 alloys having the compositions set out in Tables 2 and 3 below.
- AA3XXX has improved strength when compared to the strength of AA1050.
- the electrograining properties of AA3XXX are not as good as those of the AA1050 alloy type.
- the AA1050 alloy type is traditionally used in the European, Asian and South American markets. This alloy type electrograins well in both HCl and HNO 3 based solutions, but has a lower strength compared to other alloys. This is thought to be a potential problem in situations where alloys are to be used to form a lithographic sheet for use in longer print runs.
- the AA3XXX alloy type is traditionally used in North America. It is more difficult to electrograin this alloy type and therefore it is more often used when mechanical roughening processes may be applied.
- AA3XXX alloys can be electrograined in HCl but the electrograining process may produce surface streakiness. These alloys, thus, have relatively poor electrograining behaviour, but have a high raw strength and high bake strength.
- the wear resistance of the photosensitive coating is often improved by baking the lithographic plate. This process may, however, have an adverse effect on the strength of the aluminium substrate. This practice is more common in North America, and tends to explain the increased use of A3XXX.
- the bake strength of an alloy is typically measured using a standard bake test.
- the standard bake test involves heating the alloy for ten minutes at 240°C.
- alloys to be used for processing into lithographic sheet do not soften significantly on baking, so that the strength of the alloy is not adversely affected.
- Significant softening and the associated microstructural changes to the aluminium alloy substrate could also have a negative impact on the dimensional properties of the printing plate. This may be detrimental with respect to failure by fatigue.
- an Al alloy suitable for processing into a lithographic sheet having a composition in weight % of:
- the minimum aluminium content is 99.45 wt%. More preferably, the minimum aluminium content is 99.50 wt%.
- the versatility of the alloy is further increased when recycling after use.
- Magnesium is used to improve the graining performance of the alloy, but has a limited influence on the strength of the alloy. Magnesium does however improve the mechanical properties (such as the strength) of both the raw and baked alloy and therefore its presence in the alloy is important. However limiting the range of magnesium to 0,10 wt% is important insofar as it does not compromise the versatility of the alloy for recycling purposes.
- An alloy according to the present invention may contain up to 0.099 wt% magnesium.
- the magnesium content is within the range 0.02 to 0.05 wt%.
- Zinc also improves the graining performance of the alloy but also has limited influence on the strength of the alloy. It has been found by the inventors that a weight percentage of up to 0.05 of zinc in the aluminium alloy can have beneficial effects in respect of the electrochemical properties of the alloy.
- the minimum zinc content is 0.02 wt%.
- the ratio of zinc to magnesium in the alloy may be substantially within the range 0.1 to 2.3.
- the presence of iron in the aluminium alloy serves two purposes. The first is to ensure the formation of iron rich intermetallics which are essential for the development of a homogeneous pit structure during the electrograining (roughening) step of the plate making process. The second is to ensure that there is sufficient iron in the solid solution within the material which is beneficial for good temperature stability properties, and particularly to strength retention after plate baking.
- An advantage of the alloy having a minimum iron content is that it ensures that a sufficient number of 2nd phase intermetallics are present in the structure of the alloy. This in turn can only be achieved when the level of iron solubility in aluminium is exceeded.
- Increasing the iron content of the alloy is advantageous because iron provides a hardening effect in aluminium alloys, thus increasing the strength of the alloy.
- titanium in an aluminium alloy is necessary to ensure adequate metallurgical grain size control.
- too much titanium can have an adverse effect on the electrochemical performance of the alloy.
- the inventors have found that if the weight percentage of titanium is no more than 0.015 the alloy can benefit from the grain size control effected by the titanium, but at the same time the adverse effects on the electrochemical performance are kept to a minimum.
- An alloy according to the present invention may contain up to 0.049 wt% manganese.
- the minimum manganese content is 0.005 wt%.
- the presence of manganese in the alloy serves to increase both the raw and baked strength of the alloy.
- the manganese may have a negative impact on the electrograining behaviour of the alloy and therefore the level of manganese in the alloy should not be too high.
- the manganese content falls within the range 0.005 to 0.030 wt%.
- the manganese to magnesium ratio is substantially within the range 0.08 to 1.63.
- a lithographic sheet formed from an alloy according to the first aspect of the present invention.
- a method for processing a lithographic sheet formed from an alloy according to the first aspect of the present invention is provided.
- the tensile strength, or ultimate tensile strength/stress (UTS) is the highest load applied to a material in the course of a tensile test, divided by the original cross-sectional area of the material. In brittle or tough materials it coincides with the point of fracture, but usually extension continues under a decreasing stress after the UTS has been passed.
- proof stress is the stress required to produce a certain amount of permanent set (plastic deformation) in metals that do not exhibit a distinct yield point.
- proof stress is the stress producing a strain of 0.2% (R p 0.2).
- each of Examples 1 to 4 has a higher ultimate tensile strength in the longitudinal direction, both in the raw unbaked state and at the identified temperatures, when compared to the AA1050 group of alloys.
- the AA3XXX group of alloys does, however, have higher strength than the Examples 1 to 4.
- Figure 2 shows that each of the Examples 1 to 4 has a higher proof stress in the longitudinal direction, both in the raw unbaked state and at the identified temperatures, than the AA1050 group of alloys.
- Figure 3 shows that each of the Examples 1 to 4 has a higher ultimate tensile strength in the transverse direction, both in the raw unbaked state and at the indicated temperatures, than the AA1050 group of alloys.
- Figure 4 shows that each of the Examples 1 to 4 has a higher proof stress in the transverse direction than the AA1050 group of alloys, both in the raw state and at the temperatures indicated.
- the bend test used is a static test based on making and examining a bend which is used to fix a lithographic plate onto a printing press.
- a static test is deemed to be most appropriate, as the nature of the material (for example the alloy composition, the temper, and the method of processing the alloy) has a significant impact on the initial bend, yet a limited impact on fatigue. It is understood that failure by fatigue is mostly determined by the bend dimensions and the material gauge.
- the thickness measurements of the samples were kept as constant as possible, ranging between 0.275 and 0.280 mm.
- the inside bend radius and gauge largely determine the amount of strain on the outer surface of the bend. This can vary significantly with only a small change in set up parameters. Therefore, the inside bend radius is kept constant.
- the aluminium litho plate would be bent using a plate bender.
- a plate bender is associated with a printing press and is the piece of equipment that is used to form the bend.
- a simple bend of 60° around a set radius was made to simulate the plate bender. 60° is in the region of typically used bend angles.
- the tests were carried out in two directions, with the bend axis parallel to, and perpendicular to, the rolling direction of the plate.
- the rolling direction is the direction in which the aluminium sheet is processed during rolling.
- Figures 5 and 5a are micrographs showing a cross section of the sample of the AA1050 alloy after undergoing a bend test, as described above. It can be seen from these figures that there is inward distortion on the inner surface of the alloy caused by compressive deformation of the inner bend surface. This distortion is in the encircled area identified by the reference numeral 1. Compressive deformation can be gauged by the level of inward distortion.
- Figures 6 and 6a show a cross section of a sample of Example 1, as identified above, after undergoing a similar bend test. It can be seen from these figures that there is reduced inner bend deformation shown in area 3, and the outer surface is smoother as shown in area 4, when compared to the outer surface of the sample of AA1050 alloy shown in Figures 5 and 5a .
- Figures 7 and 8 show in more detail the outer bend surface of the sample of AA1050 alloy and a sample of Example 1, respectively. Again it can be seen from Figure 7 , in the encircled areas labelled with the reference numeral 5, that deep ridges exist in the sample of AA1050 alloy when compared to the sample of Example 1.
- Table 6 A summary of the test results is set out below in Table 6. As can be seen from the table, the AA1050 group of alloys show moderate deformation during such bend tests. It is understood that the AA3XXX group of alloys show very little deformation in bending. Table 6 Grade Level of deformation Variant + Small amount of deformation. Example 1, Example 2 +- Small to moderate amount of deformation. Example 3, Example 4 - Moderate deformation. AA1050
- the "easy" laboratory condition is achieved by electrograining for 24 seconds.
- the "intermediate" condition is achieved by electrograining for 9.5 seconds.
- the "difficult" condition is achieved by electrograining for 6.5 seconds.
- Table 8 Alloy Easy electrograining condition Intermediate electrograining condition Difficult electrograining condition AA1050 ++ + + AA3xxx -- -- -- -- Example 1 ++ ++ + Example 2 ++ ++ ++ Example 3 ++ ++ ++ Example 4 ++ ++ +
- the present invention therefore provides an aluminium alloy having improved strength compared to the AA1050 alloy type, and improved electrograining behaviour compared to the AA3XXX alloy type.
- a process for forming a lithographic sheet according to the present invention will now be briefly described.
- the process may be viewed as three sub-processes; the production of alloy and slab casting; the production of thin rolled aluminium strip; and the production of a lithographic sheet. These processes will now be described in further detail.
- Rolling sheet ingot is made by DC (direct chill) casting of molten aluminium.
- the elemental composition of the metal is controlled to the described levels by appropriate additions.
- the ingots are typically between 400-650mm in thickness.
- Scalping of the rolling sheet ingot is carried out to improve surface cleanliness and uniformity by removing the casting skin. Up to 25mm in total is removed from both surfaces.
- Pre-heating is carried out to achieve exit metal temperatures of 400-600°C for hot rolling.
- the ingot is hot rolled in multiple passes to a plate gauge of between 11-18mm thick.
- In-line quenching reduces the plate temperature to ⁇ 50°C.
- the plate is then cold rolled to an intermediate gauge.
- the target metal temperature is between 350-550°C.
- the coil can then be levelled and degreased before supply for the production of lithographic sheet.
- the surface is prepared for roughening by an alkaline-based etching process.
- Roughening is preferably achieved by electrograining. This is carried out in an electrolyte based on hydrochloric acid, or an electrolyte based on nitric acid. An AC current is applied to the electrograining bath to achieve roughening.
- the electrograined surface is anodised to improve wear resistance.
- a photosensitive coating is applied.
- the plate After the plate has been imaged, it can be baked to improve the wear resistance of the photosensitive coating.
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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)
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Abstract
Fe 0.16 to 0.40
Si up to 0.25
Cu up to 0.01
Mn up to 0.05
Ti up to 0.015
Mg 0.02 to 0.10
Zn up to 0.06
unspecified other components up to 0.03 each
Al balance, wherein the minimum Al content is 99.3.
Description
- This invention relates to an alloy suitable for processing into a lithographic sheet, to an alloy in the form of a thin rolled aluminium strip particularly for use by offset printing plate makers and to a method of processing such a lithographic sheet.
- It is known that aluminium alloy in the form of a thin rolled aluminium strip is used by offset printing plate makers.
- In order to process a thin rolled aluminium strip into a lithographic sheet, plate makers will initially degrease or etch the aluminium strip, typically in an alkaline solution. This process prepares the surface of the aluminium for graining, and evens out minor surface imperfections.
- Electrograining is then carried out to create a surface topography with convoluted hemispherical pits. This is typically carried out in an electrolyte based on hydrochloric acid, or in one based on nitric acid.
- Electrograining is carried out using an alternating current (AC) through an electrolytic cell containing the aluminium strip. The electro-chemical reactions that take place on each half cycle effectively remove aluminium from the surface by dissolution.
- Alternatively, the surface of the aluminium strip may be mechanically roughened, for example by brushing. This process is, however, less common.
- The function of the pits formed in the surface of the aluminium strip is to increase the surface area of the aluminium strip, and to hold water. In other words, due to the presence of the pits, the aluminium strip becomes hydrophilic.
- A desmutting step may then be carried out in order to remove aluminium hydroxide smut created during the electrograining process.
- Next, the aluminium strip is anodised. This results in the growth of a porous anodic oxide on the pitted surface of the aluminium strip. This provides a hard wearing coating which enhances the longevity of print quality of a lithographic sheet formed from the aluminium strip. It also enables better adhesion of the light-sensitive coating and makes the plate more chemically inert, thus improving its sheff-life.
- Normally, a photosensitive polymeric coating is then applied to the aluminium strip. This coating repels water, but attracts oil. It is required that the lithographic sheet attracts oil, since printing ink is oil-based.
- At this stage the lithographic plate comprises a hydrophilic anodised aluminium layer covered by an oleophilic photosensitive layer.
- In its simplest form, an image is created by removing parts of the coating, for example by exposure to light. This means that the coating must be easy to remove to reveal the hydrophilic anodised layer beneath. However, the coating must also be hard-wearing in order to retain a well defined image during printing runs.
- It is therefore important that the aluminium strip used to form the lithographic sheet has sufficient strength and appropriate surface functionality.
- The term "surface functionality" is used to describe the ability of a material to electrograin well in order to provide a uniform distribution in size of pits without any surface streakiness or directionality being formed. This is important for the quality of the resulting printed images.
- Most plate makers use an HCl based solution as the electrolyte during the electrograining process. However, it is also known to use an HNO3 based electrolyte. The mechanism by which the graining process proceeds is different in each electrolyte. It is advantageous for a material to electrograin well in both electrolytes.
- In the lithographic plate making industry, it is known in particular to use two alloy types. The first alloy type is known as AA1050 and has the composition set out in Table 1 below. AA1050 exhibits good electrograining behaviour.
- If a material has "good electrograining behaviour" it means that the material has the ability to produce a uniformly pitted surface under a broad range of conditions. Such a material should also be capable of electrograining in either hydrochloric acid or nitric acid based electrolytes.
Table 1 Alloy Fe% Si% Cu% Mn% Mg% Zn% Ti% V% Others % Al% AA1050 Up to 0.40 Up to 0.25 Up to 0.05 Up to 0.05 Up to 0.05 Up to 0.05 Up to 0.03 Up to 0.05 Up to 0.03 99.50 min AA1050A Up to 0.40 Up to 0.25 Up to 0.05 Up to 0.05 Up to 0.05 Up to 0.07 Up to 0.05 Not defined Up to 0.03 99.50 min - A second alloy type is known as AA3XXX and comprises AA3103 or AA3003 alloys having the compositions set out in Tables 2 and 3 below. AA3XXX has improved strength when compared to the strength of AA1050. However the electrograining properties of AA3XXX are not as good as those of the AA1050 alloy type.
-
Table 2 Alloy Fe% Si% Cu% Mn% Mg% Zn% Zr + Ti % Cr% Others % Al% AA3103 Up to 0.7 Up to 0.50 Up to 0.10 0.9 - 1.5 Up to 0.30 Up to 0.20 Up to 0.10 Up to 0.10 Up to 0.05 each, up to 0.15 total Balance -
Table 3 Alloy Fe% Si% Cu% Mn% Mg% Zn% Ti% Others Al AA3003 Up to 0.7 Up to 0.6 0.05-0.20 1.0-1.5 Not defined Up to 0.10 Not defined Up to 0.05% each, 0.15% total Balance - The AA1050 alloy type is traditionally used in the European, Asian and South American markets. This alloy type electrograins well in both HCl and HNO3 based solutions, but has a lower strength compared to other alloys. This is thought to be a potential problem in situations where alloys are to be used to form a lithographic sheet for use in longer print runs.
- The AA3XXX alloy type is traditionally used in North America. It is more difficult to electrograin this alloy type and therefore it is more often used when mechanical roughening processes may be applied.
- AA3XXX alloys can be electrograined in HCl but the electrograining process may produce surface streakiness. These alloys, thus, have relatively poor electrograining behaviour, but have a high raw strength and high bake strength.
- The wear resistance of the photosensitive coating is often improved by baking the lithographic plate. This process may, however, have an adverse effect on the strength of the aluminium substrate. This practice is more common in North America, and tends to explain the increased use of A3XXX.
- The bake strength of an alloy is typically measured using a standard bake test. The standard bake test involves heating the alloy for ten minutes at 240°C.
- It is important that alloys to be used for processing into lithographic sheet do not soften significantly on baking, so that the strength of the alloy is not adversely affected. Significant softening and the associated microstructural changes to the aluminium alloy substrate could also have a negative impact on the dimensional properties of the printing plate. This may be detrimental with respect to failure by fatigue.
- In general it has been found that an alloy exhibiting good electrograining behaviour may not have the required strength, whereas an alloy having the required strength may have poor electrograining behaviour.
- According to a first aspect of the present invention there is provided an Al alloy suitable for processing into a lithographic sheet, the alloy having a composition in weight % of:
- Fe 0.16 to 0.40
- Si up to 0.25
- Cu up to 0.01
- Mn up to 0.05
- Ti up to 0.015
- Mg 0.02 to 0.10
- Zn up to 0.06
- By having a high percentage of aluminium in the alloy, there is a correspondingly lower level of other components. This results in an alloy that is more versatile when recycling after use.
- Preferably, the minimum aluminium content is 99.45 wt%. More preferably, the minimum aluminium content is 99.50 wt%.
- By having a higher percentage weight of aluminium in the alloy, the versatility of the alloy is further increased when recycling after use.
- Magnesium is used to improve the graining performance of the alloy, but has a limited influence on the strength of the alloy. Magnesium does however improve the mechanical properties (such as the strength) of both the raw and baked alloy and therefore its presence in the alloy is important. However limiting the range of magnesium to 0,10 wt% is important insofar as it does not compromise the versatility of the alloy for recycling purposes.
- An alloy according to the present invention may contain up to 0.099 wt% magnesium.
- Preferably, the magnesium content is within the range 0.02 to 0.05 wt%.
- Zinc also improves the graining performance of the alloy but also has limited influence on the strength of the alloy. It has been found by the inventors that a weight percentage of up to 0.05 of zinc in the aluminium alloy can have beneficial effects in respect of the electrochemical properties of the alloy.
- Advantageously, the minimum zinc content is 0.02 wt%.
- The ratio of zinc to magnesium in the alloy may be substantially within the range 0.1 to 2.3.
- It has been found that by controlling the zinc and magnesium content, it is possible for the resulting aluminium alloy to have good electrograining behaviour.
- The presence of iron in the aluminium alloy serves two purposes. The first is to ensure the formation of iron rich intermetallics which are essential for the development of a homogeneous pit structure during the electrograining (roughening) step of the plate making process. The second is to ensure that there is sufficient iron in the solid solution within the material which is beneficial for good temperature stability properties, and particularly to strength retention after plate baking.
- An advantage of the alloy having a minimum iron content is that it ensures that a sufficient number of 2nd phase intermetallics are present in the structure of the alloy. This in turn can only be achieved when the level of iron solubility in aluminium is exceeded.
- Increasing the iron content of the alloy is advantageous because iron provides a hardening effect in aluminium alloys, thus increasing the strength of the alloy.
- However, it is not advantageous to increase iron beyond the upper limit of 0.4 % because such further addition provides no further positive effect on the alloy structure and minimal further increase in strength. A further disadvantage of increasing the iron content beyond 0.4 wt% is that it compromises the versatility of the alloy for recycling purposes.
- It has been found that the presence of copper in an aluminium alloy can affect the roughened pit morphology, but on the other hand can improve the material strength in both the raw and baked conditions. The inventors have found that if the weight percentage of copper is kept to 0.01 or less, the alloy can benefit from improved strength due to the presence of the copper, whilst at the same time the adverse effects of copper on the pit morphology are kept to a minimum.
- The presence of titanium in an aluminium alloy is necessary to ensure adequate metallurgical grain size control. However, too much titanium can have an adverse effect on the electrochemical performance of the alloy. The inventors have found that if the weight percentage of titanium is no more than 0.015 the alloy can benefit from the grain size control effected by the titanium, but at the same time the adverse effects on the electrochemical performance are kept to a minimum.
- An alloy according to the present invention may contain up to 0.049 wt% manganese.
- Preferably, the minimum manganese content is 0.005 wt%.
- The presence of manganese in the alloy serves to increase both the raw and baked strength of the alloy. However, the manganese may have a negative impact on the electrograining behaviour of the alloy and therefore the level of manganese in the alloy should not be too high.
- Preferably, the manganese content falls within the range 0.005 to 0.030 wt%.
- Advantageously, the manganese to magnesium ratio is substantially within the range 0.08 to 1.63.
- According to a second aspect of the present invention, there is provided a lithographic sheet formed from an alloy according to the first aspect of the present invention.
- According to a third aspect of the present invention, there is provided a method for processing a lithographic sheet formed from an alloy according to the first aspect of the present invention.
- The invention will now be described by way of example only, with reference to the examples set out below.
- Set out below are details of the composition of four examples of preferred embodiments of the invention showing the weight percentage of components forming the alloy.
Table 4 Alloy Al Fe Si Cu Mn Ti Mg Zn Others Example 1 99.48 0.36 0.08 0.001 0.009 0.006 0.046 0.022 0.005 Example 2 99.44 0.33 0.05 0.001 0.049 0.008 0.048 0.060 0.008 Example 3 99.39 0.35 0.06 0.001 0.049 0.009 0.080 0.053 0.007 Example 4 99.52 0.33 0.06 0.001 0.009 0.008 0.045 0.022 0.007 - The invention will be further described by way of non-limiting example only with reference to the accompanying figures, in which:
-
Figure 1 is a graphical representation showing the ultimate tensile strength in the longitudinal direction of examples 1, 2, 3 and 4 identified above, in a raw, unbaked state and after having been baked at each of 200°C, 220°C, 240°C and 260°C for ten minutes, compared to known alloy groups AA3XXX and AA1050. -
Figure 2 is a graphical representation showing the proof stress (Rp) in the longitudinal direction of examples 1, 2, 3 and 4 identified above, in a raw, unbaked state and after having been baked at each of 200°C, 220°C, 240°C and 260°C for ten minutes, compared to known alloy group AA1050. -
Figure 3 is a graphical representation showing the ultimate tensile strength in the transverse direction of examples 1, 2, 3 and 4 identified above, in a raw, unbaked state and after having been baked at each of 200°C, 220°C, 240°C and 260°C for ten minutes, compared to known alloy group AA1050. -
Figure 4 is a graphical representation showing the proof stress (Rp) in the transverse direction of examples 1, 2, 3 and 4 identified above, in a raw, unbaked state and after having been baked at each of 200°C, 220°C, 240°C and 260°C for ten minutes, compared to known alloy group AA1050. -
Figures 5 and5a are micrographs, each showing a cross section of a sample of an AA1050 alloy after undergoing a bend test.Figure 5 is at a magnification of x200 andFigure 5a is at a magnification of x100. -
Figures 6 and6a are micrographs, each showing a cross section of a sample of Example 1, identified above, after undergoing a bend test.Figure 6 is at a magnification of x200 andfigure 6a is at a magnification of x100. -
Figure 7 is a micrograph showing the outer bend surface in more detail of the sample of AA1050 shown inFigure 5 ; and is at a magnification of x112.5. -
Figure 8 is a micrograph showing the outer bend surface in more detail of the sample of Example 1 shown inFigure 6 .Figure 8 is at a magnification of x112.5. - The tensile strength, or ultimate tensile strength/stress (UTS) is the highest load applied to a material in the course of a tensile test, divided by the original cross-sectional area of the material. In brittle or tough materials it coincides with the point of fracture, but usually extension continues under a decreasing stress after the UTS has been passed.
- The proof stress (Rp) is the stress required to produce a certain amount of permanent set (plastic deformation) in metals that do not exhibit a distinct yield point. In the attached
Figures 2 and4 , proof stress is the stress producing a strain of 0.2% (Rp 0.2). - As mentioned above, the standard bake test is ten minutes at 240°C. In
Figures 1 to 4 , additional temperatures, namely 200, 220 and 260°C, are also examined in order to show the behaviour of strength of each alloy, and how it reduces with different bake conditions. - As shown in
Figure 1 , each of Examples 1 to 4 has a higher ultimate tensile strength in the longitudinal direction, both in the raw unbaked state and at the identified temperatures, when compared to the AA1050 group of alloys. The AA3XXX group of alloys does, however, have higher strength than the Examples 1 to 4. -
Figure 2 shows that each of the Examples 1 to 4 has a higher proof stress in the longitudinal direction, both in the raw unbaked state and at the identified temperatures, than the AA1050 group of alloys. -
Figure 3 shows that each of the Examples 1 to 4 has a higher ultimate tensile strength in the transverse direction, both in the raw unbaked state and at the indicated temperatures, than the AA1050 group of alloys. -
Figure 4 shows that each of the Examples 1 to 4 has a higher proof stress in the transverse direction than the AA1050 group of alloys, both in the raw state and at the temperatures indicated. - Bend properties are perceived to be more important than strength in terms of press performance, but are not as straightforward to measure. Therefore, strength is often used as an approximate guideline. However, simple bending tests have been carried out on the identified examples.
- The bend test used is a static test based on making and examining a bend which is used to fix a lithographic plate onto a printing press.
- A static test is deemed to be most appropriate, as the nature of the material (for example the alloy composition, the temper, and the method of processing the alloy) has a significant impact on the initial bend, yet a limited impact on fatigue. It is understood that failure by fatigue is mostly determined by the bend dimensions and the material gauge.
- In order to carry out bend tests, a plate formed from a particular alloy was bent to a strict set of parameters. If the dimensions vary too much from the designated values, including a specified gauge, then this could compromise the test results.
- The thickness measurements of the samples were kept as constant as possible, ranging between 0.275 and 0.280 mm.
- The inside bend radius and gauge largely determine the amount of strain on the outer surface of the bend. This can vary significantly with only a small change in set up parameters. Therefore, the inside bend radius is kept constant.
- In use, the aluminium litho plate would be bent using a plate bender. A plate bender is associated with a printing press and is the piece of equipment that is used to form the bend. In this test, a simple bend of 60° around a set radius was made to simulate the plate bender. 60° is in the region of typically used bend angles.
- The tests were carried out in two directions, with the bend axis parallel to, and perpendicular to, the rolling direction of the plate. The rolling direction is the direction in which the aluminium sheet is processed during rolling.
- The tests were compared to tests carried out on the AA1050 group of alloys.
- Once the tests had been carried out, a bend in an alloy was evaluated in terms of its cross sectional and outer surface appearance using optical microscopy.
- Micrographs showing bend test data for a sample of a AA1050 alloy and for a sample of Example 1 as identified above are shown in
Figures 5 to 8 . -
Figures 5 and5a are micrographs showing a cross section of the sample of the AA1050 alloy after undergoing a bend test, as described above. It can be seen from these figures that there is inward distortion on the inner surface of the alloy caused by compressive deformation of the inner bend surface. This distortion is in the encircled area identified by thereference numeral 1. Compressive deformation can be gauged by the level of inward distortion. - It can also be seen that there are ridges formed on the outer surface of the alloy by shear deformation on the outer surface, as shown in
area 2. The level of shear deformation can be gauged by the depth of the ridges formed. - It is believed to be an advantage for a material not to form deformation ridges. This is because it is thought that the ridges could behave as concentrators of stress and act as a weak point for the initiation of printing plate failure.
-
Figures 6 and6a show a cross section of a sample of Example 1, as identified above, after undergoing a similar bend test. It can be seen from these figures that there is reduced inner bend deformation shown inarea 3, and the outer surface is smoother as shown inarea 4, when compared to the outer surface of the sample of AA1050 alloy shown inFigures 5 and5a . -
Figures 7 and8 show in more detail the outer bend surface of the sample of AA1050 alloy and a sample of Example 1, respectively. Again it can be seen fromFigure 7 , in the encircled areas labelled with thereference numeral 5, that deep ridges exist in the sample of AA1050 alloy when compared to the sample of Example 1. - An analysis of micrographs such as those shown in
Figures 5 to 8 is largely qualitative. Nevertheless the levels of shear deformation and cracking observed varied between different materials allowing for a straightforward comparison between the different alloys. Roughness measurements were also carried out on the outer surface of the bend for each alloy, and the maximum peak to trough distances of the shear deformation ridges on the outer surface of the bends were measured. - These topographical measurements of the outer bend surface were made using a white light interferometer. In this application interferometery is used as a non-contact method of measuring surface roughness.
- The results of the roughness measurements are set out in Table 5 below.
Table 5 Variant Maximum peak to trough distance (µm) Example 1 13 Example 2 11 Example 3 16 Example 4 17 AA1050 19 - A summary of the test results is set out below in Table 6. As can be seen from the table, the AA1050 group of alloys show moderate deformation during such bend tests. It is understood that the AA3XXX group of alloys show very little deformation in bending.
Table 6 Grade Level of deformation Variant + Small amount of deformation. Example 1, Example 2 +- Small to moderate amount of deformation. Example 3, Example 4 - Moderate deformation. AA1050 - As explained above, it is important that a uniformly pitted and streak free surface is achieved by electrograining the alloy in either a solution based on hydrochloric acid, or one based on nitric acid, to produce a surface having good functionality.
- The electrograining performance of the Examples 1 to 4 compared to both the AA1050 and the AA3XXX group of alloys is set out below.
- The results described below are based on laboratory testing of alloys in an HCl based electrolyte.
- The following scale of measuring electrograining performance has been used.
Table 7 Grade Electrograining Comment ++ Very good This is the target electrograining performance, with high uniformity and ease of initiation. + Good This is the industry-accepted benchmark for electrograining performance. +- Adequate This indicates a slight deterioration in uniformity, but is still considered acceptable. - Poor This indicates a noticeable deterioration in uniformity and initiation. This would suggest that there could be problems on an industrial scale. -- Very poor This indicates poor performance, as incomplete electrograining would be seen on the laboratory scale. - The results for the different Examples are given below.
- All conditions use a charge density of 1000 C/dm2, but the electrograining is carried out for different lengths of time.
- The "easy" laboratory condition is achieved by electrograining for 24 seconds.
- The "intermediate" condition is achieved by electrograining for 9.5 seconds.
- The "difficult" condition is achieved by electrograining for 6.5 seconds.
Table 8 Alloy Easy electrograining condition Intermediate electrograining condition Difficult electrograining condition AA1050 ++ + + AA3xxx -- -- -- Example 1 ++ ++ + Example 2 ++ ++ ++ Example 3 ++ ++ ++ Example 4 ++ ++ + - The results show that each of the Examples 1 to 4 has electrograining properties at least as good as, and under certain conditions, better than the AA1050 group of alloys.
- The electrograining behaviour of each of Examples 1 to 4 is, in all cases better than that of the AA3XXX alloy group.
- The present invention therefore provides an aluminium alloy having improved strength compared to the AA1050 alloy type, and improved electrograining behaviour compared to the AA3XXX alloy type.
- A process for forming a lithographic sheet according to the present invention will now be briefly described. The process may be viewed as three sub-processes; the production of alloy and slab casting; the production of thin rolled aluminium strip; and the production of a lithographic sheet. These processes will now be described in further detail.
- Rolling sheet ingot is made by DC (direct chill) casting of molten aluminium.
- The elemental composition of the metal is controlled to the described levels by appropriate additions.
- The ingots are typically between 400-650mm in thickness.
- Scalping of the rolling sheet ingot is carried out to improve surface cleanliness and uniformity by removing the casting skin. Up to 25mm in total is removed from both surfaces.
- Pre-heating is carried out to achieve exit metal temperatures of 400-600°C for hot rolling.
- The ingot is hot rolled in multiple passes to a plate gauge of between 11-18mm thick.
- In-line quenching reduces the plate temperature to <50°C.
- The plate is then cold rolled to an intermediate gauge.
- Batch inter-annealing can be carried out. The target metal temperature is between 350-550°C.
- Further cold rolling steps are used to achieve the final product thickness of between 0.1-0.5mm.
- The coil can then be levelled and degreased before supply for the production of lithographic sheet.
- The surface is prepared for roughening by an alkaline-based etching process.
- Roughening is preferably achieved by electrograining. This is carried out in an electrolyte based on hydrochloric acid, or an electrolyte based on nitric acid. An AC current is applied to the electrograining bath to achieve roughening.
- The electrograined surface is anodised to improve wear resistance.
- Various other in-line treatments may be applied to improve plate properties between some or each of the described basic process steps.
- A photosensitive coating is applied.
- After the plate has been imaged, it can be baked to improve the wear resistance of the photosensitive coating.
Al balance, wherein the minimum Al content is 99.3.
Claims (13)
- An Al alloy suitable for processing into a lithographic sheet, the alloy having a composition in weight % of:Fe 0.16 to 0.40Si up to 0.25Cu up to 0.01Mn up to 0.05Ti up to 0.015Mg 0.02 to 0.10Zn up to 0.06unspecified other components up to 0.03 eachAl balance, wherein the minimum Al content is 99.3.
- An alloy according to Claim 1 wherein the minimum aluminium (Al) content is 99.45 wt%.
- An alloy according to Claim 1 or Claim 2 wherein the minimum aluminium content is 99.50 wt%.
- An alloy according to any one of the preceding claims containing up to 0.099 wt% magnesium.
- An alloy according to any one of the preceding claims wherein the magnesium content is preferably within the range 0.02 to 0.05 wt%.
- An alloy according to any one of the preceding claims wherein the minimum zinc (Zn) content is 0.02 wt%.
- An alloy according to any one of the preceding claims, wherein the ratio of zinc to magnesium in the alloy is substantially within the range 0.1 to 2.3.
- An alloy according to any one of the preceding claims containing up to 0.049 wt% manganese.
- An alloy according to any one of the preceding claims wherein the minimum manganese (Mn) content is 0.005 wt%.
- An alloy according to any one of the preceding claims wherein the manganese (Mn) content falls within the range 0.005 to 0.030 wt%.
- An alloy according to any one of the preceding claims wherein the manganese to magnesium ratio is substantially within the range 0.08 to 1.63.
- A lithographic sheet formed from an alloy according to any one of the preceding claims.
- A method of processing a lithographic sheet according to Claim 12.
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GB0811534A GB2461240A (en) | 2008-06-24 | 2008-06-24 | Aluminium alloy for lithographic sheet |
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EP2138592A3 EP2138592A3 (en) | 2012-05-23 |
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EP (1) | EP2138592A3 (en) |
JP (1) | JP2010012779A (en) |
CN (1) | CN101613821A (en) |
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JP2013177685A (en) * | 2013-04-11 | 2013-09-09 | Kobe Steel Ltd | High strength aluminum alloy sheet for automatic plate-making printing plate |
CN104073690A (en) * | 2014-06-18 | 2014-10-01 | 厦门厦顺铝箔有限公司 | Aluminum alloy product and manufacture method thereof |
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US726734A (en) * | 1901-09-27 | 1903-04-28 | Rowland Telegraphic Company | Electric circuit. |
JPS5842745A (en) * | 1981-09-03 | 1983-03-12 | Furukawa Alum Co Ltd | Aluminum alloy plate for printing and its manufacture |
JP2778662B2 (en) * | 1996-04-05 | 1998-07-23 | 株式会社神戸製鋼所 | Aluminum alloy plate for printing plate and method for producing the same |
JP3915944B2 (en) * | 1997-08-22 | 2007-05-16 | 古河スカイ株式会社 | Method for producing aluminum alloy support for lithographic printing plate and aluminum alloy support for lithographic printing plate |
JP3887497B2 (en) * | 1998-09-21 | 2007-02-28 | 株式会社神戸製鋼所 | Aluminum alloy plate for surface treatment and manufacturing method thereof |
ES2312341T3 (en) * | 1999-05-27 | 2009-03-01 | Novelis, Inc. | ALUMINUM ALLOY SHEET. |
DE29924474U1 (en) * | 1999-07-02 | 2003-08-28 | Hydro Aluminium Deutschland | litho |
US6568325B2 (en) * | 2000-03-28 | 2003-05-27 | Fuji Photo Film Co., Ltd. | Supports for lithographic printing plates |
JP3882987B2 (en) * | 2000-07-11 | 2007-02-21 | 三菱アルミニウム株式会社 | Aluminum alloy plate for lithographic printing plates |
EP1176031B1 (en) * | 2000-07-17 | 2004-04-07 | Agfa-Gevaert | Production of support for lithographic printing plate |
ES2259311T3 (en) * | 2000-12-11 | 2006-10-01 | Novelis, Inc. | ALUMINUM ALLOY FOR LITHOGRAPHIC IRON. |
JP2002363799A (en) * | 2001-06-11 | 2002-12-18 | Fuji Photo Film Co Ltd | Aluminum plate, method for producing supporting body for planographic printing plate, supporting body for planographic printing plate and planographic printing original plate |
WO2003057934A1 (en) * | 2001-12-28 | 2003-07-17 | Mitsubishi Aluminum Co., Ltd. | Aluminum alloy plate for lithographic printing form and method for production thereof and lithographic printing form |
JP4287414B2 (en) * | 2001-12-28 | 2009-07-01 | 三菱アルミニウム株式会社 | Aluminum alloy plate for lithographic printing plate and lithographic printing plate |
JP4318587B2 (en) * | 2003-05-30 | 2009-08-26 | 住友軽金属工業株式会社 | Aluminum alloy plate for lithographic printing plates |
JP4105042B2 (en) * | 2003-06-12 | 2008-06-18 | 三菱アルミニウム株式会社 | Aluminum alloy material for lithographic printing plate and method for producing the same |
JP4630968B2 (en) * | 2003-07-25 | 2011-02-09 | 三菱アルミニウム株式会社 | Aluminum alloy plate for planographic printing plate, method for producing the same and planographic printing plate |
JP4250490B2 (en) * | 2003-09-19 | 2009-04-08 | 富士フイルム株式会社 | Aluminum alloy base plate for planographic printing plate and support for planographic printing plate |
EP1543899A3 (en) * | 2003-12-17 | 2005-12-21 | Fuji Photo Film B.V. | Aluminium alloy substrate for digitally imageable lithographic printing plate and process for producing the same |
JP4161134B2 (en) * | 2004-06-25 | 2008-10-08 | 日本軽金属株式会社 | Method for producing aluminum alloy base plate for printing plate |
JP2006205557A (en) * | 2005-01-28 | 2006-08-10 | Fuji Photo Film Co Ltd | Substrate for lithographic printing plate |
WO2006134542A2 (en) * | 2005-06-15 | 2006-12-21 | Hulett Aluminium (Proprietary) Limited | Aluminium alloy for lithographic sheet and process for producing the same |
US9914318B2 (en) * | 2005-10-19 | 2018-03-13 | Hydro Aluminium Deutschland Gmbh | Aluminum strip for lithographic printing plate supports |
JP2007175867A (en) * | 2005-12-26 | 2007-07-12 | Fujifilm Corp | Method of manufacturing support for lithographic printing plate, support for lithographic printing plate and lithographic printing original plate |
JP4913008B2 (en) * | 2007-10-12 | 2012-04-11 | 三菱アルミニウム株式会社 | Aluminum alloy material for lithographic printing and method for producing the same |
CN101182611B (en) * | 2007-12-11 | 2010-10-13 | 乳源东阳光精箔有限公司 | Aluminum plate foundation for printing master and manufacturing method therefor |
-
2008
- 2008-06-24 GB GB0811534A patent/GB2461240A/en not_active Withdrawn
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2009
- 2009-06-23 US US12/489,908 patent/US20100034694A1/en not_active Abandoned
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- 2009-06-24 TW TW098121098A patent/TWI405856B/en not_active IP Right Cessation
- 2009-06-24 CN CN200910139487A patent/CN101613821A/en active Pending
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EP2138592A3 (en) | 2012-05-23 |
CN101613821A (en) | 2009-12-30 |
GB0811534D0 (en) | 2008-07-30 |
GB2461240A (en) | 2009-12-30 |
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TW201012942A (en) | 2010-04-01 |
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