CA2582249A1 - High hardness aluminium moulding plate and method for producing said plate - Google Patents
High hardness aluminium moulding plate and method for producing said plate Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
Abstract
Moulding plate of an aluminium wrought alloy comprising, in weight percent: Si 1.4-2.1, Mn 0.8-1.2, Cu 0.45-0.9, Mg 0.7-1.2, Ti <0.15, Zn <0.4, Fe <0.7, one or more of Zr, Cr, V each <0.25, incidental elements and impurities, each <0.05, total <0.25, the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105HB.
Description
HIGH HARDNESS ALUMINIUM MOULDING PLATE AND METHOD FOR PRODUCING SAID PLATE
The invention relates to moulding plate of an aluminium wrought alloy. The invention further relates to a method for producing said moulding plate.
In the tooling and moulding plate market for blow moulding and thermoforming of rubbers and plastic, a sustained effort in reducing costs is made whilst maintaining satisfactory wear resistance and repair weldability. These types of tooling plates are also widely used in many other industrial applications, including components produced by various machining operations such as drilling, milling and turning.
Commonly used tooling plates are made from selected alloys from the AA2000 series alloys, the AA6000 series alloys or the AA7000-series alloys.
High wear resistance in combination with good machinability are important properties of alloys for moulding plate. In typical tooling plate wrought alloys this wear resistance is obtained by alloying with copper (such as in the AA2000 series) or Zinc (such as in the AA7000 series) or magnesium and silicon (such as in the AA6000 series) in combination with a thermo-mechanical treatment. In these heat treatable alloy classes, the typical way to achieve high hardness is via precipitation hardening of coherent phases. Additional hardening by relatively coarse particles, such as primary Si and incoherent Mg2Si is often considered inappropriate, because of the related risks of eutectic melting at elevated temperatures. Also additional hardening by a-AI(Fe,Mn,Cu)Si dispersoids is not readily applied, since it is generally believed that they increase the quench sensitivity of the alloy. Increased quench sensitivity is considered a disadvantageous characteristic, in particular for thicker gauge products.
Typically, with AA2000 and AA7000 alloys, higher hardness is achieved than with AA6000 alloys. However, a disadvantage of the AA2000 series is the high copper content which makes the alloy expensive as well as very sensitive to the heat treatment. Also, the weldability of the alloy is adversely affected by the high copper content. Similar arguments are made for the AA7000 series such as high residual stresses, and poor weldability and corrosion performance which cause complications with dimensional tolerances, repair weldability, and durability of the mould.
The wear resistance of an AA6000 series alloy in a T6 temper, such as AA6010, AA6013, AA6061, AA6066, AA6070 and AA6082 is usually adequate for normal industrial applications. However, for high performance applications a higher wear resistance is desired, without adversely affecting weldability and costs.
CONFIRMATION COPY
The invention relates to moulding plate of an aluminium wrought alloy. The invention further relates to a method for producing said moulding plate.
In the tooling and moulding plate market for blow moulding and thermoforming of rubbers and plastic, a sustained effort in reducing costs is made whilst maintaining satisfactory wear resistance and repair weldability. These types of tooling plates are also widely used in many other industrial applications, including components produced by various machining operations such as drilling, milling and turning.
Commonly used tooling plates are made from selected alloys from the AA2000 series alloys, the AA6000 series alloys or the AA7000-series alloys.
High wear resistance in combination with good machinability are important properties of alloys for moulding plate. In typical tooling plate wrought alloys this wear resistance is obtained by alloying with copper (such as in the AA2000 series) or Zinc (such as in the AA7000 series) or magnesium and silicon (such as in the AA6000 series) in combination with a thermo-mechanical treatment. In these heat treatable alloy classes, the typical way to achieve high hardness is via precipitation hardening of coherent phases. Additional hardening by relatively coarse particles, such as primary Si and incoherent Mg2Si is often considered inappropriate, because of the related risks of eutectic melting at elevated temperatures. Also additional hardening by a-AI(Fe,Mn,Cu)Si dispersoids is not readily applied, since it is generally believed that they increase the quench sensitivity of the alloy. Increased quench sensitivity is considered a disadvantageous characteristic, in particular for thicker gauge products.
Typically, with AA2000 and AA7000 alloys, higher hardness is achieved than with AA6000 alloys. However, a disadvantage of the AA2000 series is the high copper content which makes the alloy expensive as well as very sensitive to the heat treatment. Also, the weldability of the alloy is adversely affected by the high copper content. Similar arguments are made for the AA7000 series such as high residual stresses, and poor weldability and corrosion performance which cause complications with dimensional tolerances, repair weldability, and durability of the mould.
The wear resistance of an AA6000 series alloy in a T6 temper, such as AA6010, AA6013, AA6061, AA6066, AA6070 and AA6082 is usually adequate for normal industrial applications. However, for high performance applications a higher wear resistance is desired, without adversely affecting weldability and costs.
CONFIRMATION COPY
It is an object of the invention to provide a moulding plate of an aluminium wrought alloy with an improved resistance to wear.
According to the invention, this object is reached by providing a moulding plate of an aluminium wrought alloy comprising, in weight percent:
- Si 1.4 - 2.1 - Mn 0.8-1.2 - Cu 0.45-0.9 - Mg 0.7-1.2 - Ti <0.15 - Zn <0.4 - Fe <0.7 - one or more of Zr, Cr, V each <0.25, total preferably < 0.35 - incidental elements and impurities, each <0.05, total <0.25, - the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105HB.
The increased hardness is reached by combining precipitation hardening of Mg-Si-Cu phases, Fe- and Mn-containing intermetallics and dispersoids, which are known to actually reduce the age hardening effect in balanced AIMgSi(Cu) alloys through their effect on the quench sensitivity, with a high excess of Si, which decreases the Mg solute level, to minimise the negative effect of Mn-containing dispersoids on the quench sensitivity. The supersaturation level for Mg-Si phases is not yet so high that particularly high quench sensitivities already result from the Mg-, Si-, and Cu solute content. The balanced alloy composition according to the invention is believed to combine the strength increasing effect of a silicon addition with moderate amount of copper, magnesium and manganese. It was found that this alloy provides satisfactory weldability and a hardness of at least 105 HB. It should be noted that the hardness values are expressed in the Brinell scale and were measured by a ball having a 2.5 mm diameter loaded with a mass of 62.5 kg. The hardness tests were performed according to ASTM E10 (version 2002).
In a preferred embodiment of the invention the hardness in T6 temper condition is at least 115HB, more preferably at least 120HB. These hardness values imply an increased machinability as well as wear resistance. The chemical composition in combination with a heat treatment ensures that adequate weldability and thus reparability is maintained: surprisingly it has been found that for Cu levels of up to 0.9% the plate alloy shows very good reparability with for instance a common 4043 filler wire.
In an embodiment the Si is in the range of 1.53 - 2.0 %, more preferably in the range of 1.55-1.9 %. It was found that this range of silicon provides a very good combination of the desirable properties, through hardening by coherent Mg-Si-Cu phases, and by primary Si, incoherent Mg2Si and a-AI(Fe,Mn,Cu)Si intermetallic phases and dispersoids.
In an embodiment the Mn is in the range of 0.85 - 1.10 %. It was found that this range of manganese provides a very good combination of the desirable properties, in particular by stimulating the formation of a-AI(Fe,Mn,Cu)Si intermetallic phases and dispersoids. At high Si levels, the tendency to form the relatively brittle (3-AIFeSi intermetallic phase increases. However, by ensuring the presence of suitable amounts of Mn and Cu the more favourable a-AI(Fe,Mn,Cu)Si phase is stabilised.
In an embodiment the Cu is in the range of 0.5 - 0.7 %. It was found that this range of copper provides a very good combination of the desirable properties through coherent Mg-Si-Cu phases and stabilised a-AI(Fe,Mn,Cu)Si, whilst keeping alloying cost down and ensuring good repair weldabiRy.
In an embodiment the Zn is below 0.3%, preferably in the range of 0.17 - 0.3 In an embodiment the Fe is preferably at least 0.2%, more preferably in the range 0.2 - 0.5%, and even more preferably in the range 0.3 - 0.5% to ensure the formation of sufficient amounts of hardness increasing a-AI(Fe,Mn,Cu)Si intermetallics.
In an embodiment the Zr, Cr, V are each preferably below 0.18%, more preferably below 0.12% to further reduce the quench sensitivity.
In an embodiment the moulding plate has a machinability rating of "B" or better as defined in 'ASM Specialty Handbook - Aluminium and Aluminium Alloys (ed.
J.R.
Davis), ASM International 1993, page 328-331.
In an embodiment the moulding plate has a final thickness of 300 mm, in which the claimed hardness values can still be met in the plate centre. Preferably the final thickness is in the range of between 5 to 300 mm, more preferably in the range of between 5 to 260 mm. These thickness ranges allow the application of the moulding plate for all practical application involving moulding plate.
According to the invention, this object is reached by providing a moulding plate of an aluminium wrought alloy comprising, in weight percent:
- Si 1.4 - 2.1 - Mn 0.8-1.2 - Cu 0.45-0.9 - Mg 0.7-1.2 - Ti <0.15 - Zn <0.4 - Fe <0.7 - one or more of Zr, Cr, V each <0.25, total preferably < 0.35 - incidental elements and impurities, each <0.05, total <0.25, - the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105HB.
The increased hardness is reached by combining precipitation hardening of Mg-Si-Cu phases, Fe- and Mn-containing intermetallics and dispersoids, which are known to actually reduce the age hardening effect in balanced AIMgSi(Cu) alloys through their effect on the quench sensitivity, with a high excess of Si, which decreases the Mg solute level, to minimise the negative effect of Mn-containing dispersoids on the quench sensitivity. The supersaturation level for Mg-Si phases is not yet so high that particularly high quench sensitivities already result from the Mg-, Si-, and Cu solute content. The balanced alloy composition according to the invention is believed to combine the strength increasing effect of a silicon addition with moderate amount of copper, magnesium and manganese. It was found that this alloy provides satisfactory weldability and a hardness of at least 105 HB. It should be noted that the hardness values are expressed in the Brinell scale and were measured by a ball having a 2.5 mm diameter loaded with a mass of 62.5 kg. The hardness tests were performed according to ASTM E10 (version 2002).
In a preferred embodiment of the invention the hardness in T6 temper condition is at least 115HB, more preferably at least 120HB. These hardness values imply an increased machinability as well as wear resistance. The chemical composition in combination with a heat treatment ensures that adequate weldability and thus reparability is maintained: surprisingly it has been found that for Cu levels of up to 0.9% the plate alloy shows very good reparability with for instance a common 4043 filler wire.
In an embodiment the Si is in the range of 1.53 - 2.0 %, more preferably in the range of 1.55-1.9 %. It was found that this range of silicon provides a very good combination of the desirable properties, through hardening by coherent Mg-Si-Cu phases, and by primary Si, incoherent Mg2Si and a-AI(Fe,Mn,Cu)Si intermetallic phases and dispersoids.
In an embodiment the Mn is in the range of 0.85 - 1.10 %. It was found that this range of manganese provides a very good combination of the desirable properties, in particular by stimulating the formation of a-AI(Fe,Mn,Cu)Si intermetallic phases and dispersoids. At high Si levels, the tendency to form the relatively brittle (3-AIFeSi intermetallic phase increases. However, by ensuring the presence of suitable amounts of Mn and Cu the more favourable a-AI(Fe,Mn,Cu)Si phase is stabilised.
In an embodiment the Cu is in the range of 0.5 - 0.7 %. It was found that this range of copper provides a very good combination of the desirable properties through coherent Mg-Si-Cu phases and stabilised a-AI(Fe,Mn,Cu)Si, whilst keeping alloying cost down and ensuring good repair weldabiRy.
In an embodiment the Zn is below 0.3%, preferably in the range of 0.17 - 0.3 In an embodiment the Fe is preferably at least 0.2%, more preferably in the range 0.2 - 0.5%, and even more preferably in the range 0.3 - 0.5% to ensure the formation of sufficient amounts of hardness increasing a-AI(Fe,Mn,Cu)Si intermetallics.
In an embodiment the Zr, Cr, V are each preferably below 0.18%, more preferably below 0.12% to further reduce the quench sensitivity.
In an embodiment the moulding plate has a machinability rating of "B" or better as defined in 'ASM Specialty Handbook - Aluminium and Aluminium Alloys (ed.
J.R.
Davis), ASM International 1993, page 328-331.
In an embodiment the moulding plate has a final thickness of 300 mm, in which the claimed hardness values can still be met in the plate centre. Preferably the final thickness is in the range of between 5 to 300 mm, more preferably in the range of between 5 to 260 mm. These thickness ranges allow the application of the moulding plate for all practical application involving moulding plate.
In an embodiment the moulding plate has been rolled to the final thickness by hot rolling only.
According to a further aspect of the invention, a method is provided of manufacturing a moulding plate comprising the subsequent steps of:
= casting an ingot having a composition comprising (in weight percent):
o Si 1.4 - 2.1 o Mn 0.8-1.2 o Cu 0.45 - 0.9 o Mg 0.7-1.2 o Ti <0.15 o Zn <0.4 o Fe <0.7 0 one or more of Zr, Cr, V each <0.25, total preferably < 0.35 o incidental elements and impurities, each <0.05, total <0.25, balance aluminium, and with preferred compositional ranges as set out in the description hereinabove.
= homogenising and/or preheating the ingot, = working said plate to a final thickness, preferably by hot rolling and/or cold rolling, more preferably by hot rolling only, = subjecting to heat treatment comprising solution heat treating followed by rapid cooling, = ageing, wherein the cooling rate during said rapid cooling is chosen so as to obtain a hardness of the moulding plate of at least 105 HB.
By manufacturing a moulding plate according to the invention a high hardness product with a high content of chip-breaking intermetallics is obtained. The cooling rate during the rapid cooling after solution heat treating is important because this cooling rate determines the amount of solute content of Mg, Si and Cu which were dissolved during the solution heat treatment.
In an embodiment of the invention the heat treatment after hot rolling or hot pressing is a T6-treatment.
In an embodiment the homogenisation temperature is at least 450 C, preferably at least 500 C, more preferably between 500 and 595 C, preferably for between 1 to 25 hours, more preferably for between 10 to 16 hours. The pre-heat temperature is at least 570 C, between about 300 C and 570 C, preferably between 350 and 530 C, preferably for between 1 to 25 hours, more preferably for between 1 and 10 hours.
In an embodiment the solution heat-treating temperature is at least 500 C, preferably at least 520 C and more preferably at least 540 C. In an embodiment the cooling rate after solution heat-treating from the solution heat-treating temperature to below 250 C, preferably to below 150 C and more preferably to below 100 C, is at least 1 C/s, preferably at least 2 C/s more preferably 5 C/s, even more preferably at least 10 C/s. It should be noted that the cooling.rate of the product during quenching is dependent on the location within the product. The centre of the product cools down more slowly than the surface of the product. Consequently, since the final hardness is dependent on the cooling rate, the hardness will be lower if the local cooling rate during quenching is lower. The critical point in the product is defined as the point where the cooling rate during quenching is the lowest. The abovementioned cooling rates relate to the cooling rate at the critical point.
In a further embodiment, the ageing process comprises natural ageing for a maximum duration of 28 days, preferably for a maximum duration of 14 days, more preferably for a maximum duration of 7 days, even more preferably for a maximum duration of 2 days, followed by an artificial ageing treatment equivalent to ageing at about 180'to 200 C for about 1-10 hours. It is known to the skilled person that time and temperature of an annealing are usually not chosen independently. The ageing process is thermally activated, resulting in the situation that a high temperature coupled with a short time is equivalent to a lower temperature and a longer time, i.e.
the same metallurgical state is reached after the ageing treatment.
In an embodiment of the invention the working step comprises a rolling or pressing step. In a further embodiment the rolling step comprises a hot rolling and/or a hot pressing step and/or cold-rolling step. Preferably, the working step comprises hot rolling and/or hot pressing only.
In an embodiment of the invention the casting step is a near-net shape casting step, wherein the dimensions of the cast product approximates the final product.
A particular embodiment of the invention will now be explained by the following non-limitative examples and figure. It should be noted that the chemical composition of the alloys was varied by mixing cuttings of a brazing alloy, consisting mostly of an AA3000-series core alloy clad with a Si-rich AA4000-series alloy with technical purity Al 99.0 after which Cu and/or Mg and/or other elements can be added to obtain the final chemistry.
Table 1. Average composition of tested alloys and hardness in T6-condition.
Alloy Si Fe Cu Mn Mg Zn Ti HB content brazing alloy (%) Al 99.0 0.4 0.6 0.03 0.03 0.03 0.07 - - 0 Brazing alloy 2.0 0.4 0.5 1.0 0.40 0.25 0.05 - 100 Example 1 1.72 0.37 0.61 0.77 0.97 0.21 0.05 124 82 Example 2 1.70 0.39 0.91 0.95 0.85 0.21 0.05 124 81 Example 3 2.10 0.38 0.50 1.03 0.88 0.25 0.05 124 100 Example 4 1.68 0.41 0.40 0.78 0.98 0.21 0.05 123 80 Example 5 1.71 0.43 0.51 0.76 0.70 0.21 0.05 122 82 Example 6 1.59 0.38 0.61 0.81 0.98 0.10 0.03 123 75 Example 7 1.60 0.39 0.64 0.95 0.91 0.02 0.05 Fig.1 80 These alloys were homogenised at a temperature above 510 C, optionally hot rolled, solution heat treated at 550 C, cooled down with at least 10 C/s to maximise the solute content of Mg, Si and Cu, stored for 14 days at room temperature, and aged following an ageing treatment equivalent to 190 C for 2-6 hours. In this way, a high-hardness T6-temper product with a high content of chip-breaking intermetallics is obtained, leading to a hardness of at least 120 HB. Example 7 was solution heat treated at 530 C and stored at room temperature for a period of 1 day, the remainder of the process conditions being as given above for the other alloys.
The hardness profiles of plates with the composition according to Example 7 with thicknesses of 80, 100 or 150 mm are shown in Fig. 1. Along the X-axis the distance (L) to the centre of the plate in the thickness direction in mm is given, and along the Y-axis the hardness in HB values is given at different locations over the thickness of the plate. All measured values show a hardness value of at least at every location over the thickness of the plate.
It is of course to be understood that the present invention is not limited to the described embodiments and examples described above, but encompasses any and all embodiments within the scope of the description and the following claims.
According to a further aspect of the invention, a method is provided of manufacturing a moulding plate comprising the subsequent steps of:
= casting an ingot having a composition comprising (in weight percent):
o Si 1.4 - 2.1 o Mn 0.8-1.2 o Cu 0.45 - 0.9 o Mg 0.7-1.2 o Ti <0.15 o Zn <0.4 o Fe <0.7 0 one or more of Zr, Cr, V each <0.25, total preferably < 0.35 o incidental elements and impurities, each <0.05, total <0.25, balance aluminium, and with preferred compositional ranges as set out in the description hereinabove.
= homogenising and/or preheating the ingot, = working said plate to a final thickness, preferably by hot rolling and/or cold rolling, more preferably by hot rolling only, = subjecting to heat treatment comprising solution heat treating followed by rapid cooling, = ageing, wherein the cooling rate during said rapid cooling is chosen so as to obtain a hardness of the moulding plate of at least 105 HB.
By manufacturing a moulding plate according to the invention a high hardness product with a high content of chip-breaking intermetallics is obtained. The cooling rate during the rapid cooling after solution heat treating is important because this cooling rate determines the amount of solute content of Mg, Si and Cu which were dissolved during the solution heat treatment.
In an embodiment of the invention the heat treatment after hot rolling or hot pressing is a T6-treatment.
In an embodiment the homogenisation temperature is at least 450 C, preferably at least 500 C, more preferably between 500 and 595 C, preferably for between 1 to 25 hours, more preferably for between 10 to 16 hours. The pre-heat temperature is at least 570 C, between about 300 C and 570 C, preferably between 350 and 530 C, preferably for between 1 to 25 hours, more preferably for between 1 and 10 hours.
In an embodiment the solution heat-treating temperature is at least 500 C, preferably at least 520 C and more preferably at least 540 C. In an embodiment the cooling rate after solution heat-treating from the solution heat-treating temperature to below 250 C, preferably to below 150 C and more preferably to below 100 C, is at least 1 C/s, preferably at least 2 C/s more preferably 5 C/s, even more preferably at least 10 C/s. It should be noted that the cooling.rate of the product during quenching is dependent on the location within the product. The centre of the product cools down more slowly than the surface of the product. Consequently, since the final hardness is dependent on the cooling rate, the hardness will be lower if the local cooling rate during quenching is lower. The critical point in the product is defined as the point where the cooling rate during quenching is the lowest. The abovementioned cooling rates relate to the cooling rate at the critical point.
In a further embodiment, the ageing process comprises natural ageing for a maximum duration of 28 days, preferably for a maximum duration of 14 days, more preferably for a maximum duration of 7 days, even more preferably for a maximum duration of 2 days, followed by an artificial ageing treatment equivalent to ageing at about 180'to 200 C for about 1-10 hours. It is known to the skilled person that time and temperature of an annealing are usually not chosen independently. The ageing process is thermally activated, resulting in the situation that a high temperature coupled with a short time is equivalent to a lower temperature and a longer time, i.e.
the same metallurgical state is reached after the ageing treatment.
In an embodiment of the invention the working step comprises a rolling or pressing step. In a further embodiment the rolling step comprises a hot rolling and/or a hot pressing step and/or cold-rolling step. Preferably, the working step comprises hot rolling and/or hot pressing only.
In an embodiment of the invention the casting step is a near-net shape casting step, wherein the dimensions of the cast product approximates the final product.
A particular embodiment of the invention will now be explained by the following non-limitative examples and figure. It should be noted that the chemical composition of the alloys was varied by mixing cuttings of a brazing alloy, consisting mostly of an AA3000-series core alloy clad with a Si-rich AA4000-series alloy with technical purity Al 99.0 after which Cu and/or Mg and/or other elements can be added to obtain the final chemistry.
Table 1. Average composition of tested alloys and hardness in T6-condition.
Alloy Si Fe Cu Mn Mg Zn Ti HB content brazing alloy (%) Al 99.0 0.4 0.6 0.03 0.03 0.03 0.07 - - 0 Brazing alloy 2.0 0.4 0.5 1.0 0.40 0.25 0.05 - 100 Example 1 1.72 0.37 0.61 0.77 0.97 0.21 0.05 124 82 Example 2 1.70 0.39 0.91 0.95 0.85 0.21 0.05 124 81 Example 3 2.10 0.38 0.50 1.03 0.88 0.25 0.05 124 100 Example 4 1.68 0.41 0.40 0.78 0.98 0.21 0.05 123 80 Example 5 1.71 0.43 0.51 0.76 0.70 0.21 0.05 122 82 Example 6 1.59 0.38 0.61 0.81 0.98 0.10 0.03 123 75 Example 7 1.60 0.39 0.64 0.95 0.91 0.02 0.05 Fig.1 80 These alloys were homogenised at a temperature above 510 C, optionally hot rolled, solution heat treated at 550 C, cooled down with at least 10 C/s to maximise the solute content of Mg, Si and Cu, stored for 14 days at room temperature, and aged following an ageing treatment equivalent to 190 C for 2-6 hours. In this way, a high-hardness T6-temper product with a high content of chip-breaking intermetallics is obtained, leading to a hardness of at least 120 HB. Example 7 was solution heat treated at 530 C and stored at room temperature for a period of 1 day, the remainder of the process conditions being as given above for the other alloys.
The hardness profiles of plates with the composition according to Example 7 with thicknesses of 80, 100 or 150 mm are shown in Fig. 1. Along the X-axis the distance (L) to the centre of the plate in the thickness direction in mm is given, and along the Y-axis the hardness in HB values is given at different locations over the thickness of the plate. All measured values show a hardness value of at least at every location over the thickness of the plate.
It is of course to be understood that the present invention is not limited to the described embodiments and examples described above, but encompasses any and all embodiments within the scope of the description and the following claims.
Claims (10)
1. Moulding plate of an aluminium wrought alloy comprising, in weight percent:
- Si 1 4 - 2.1 - Mn 0 8 - 1 2 - Cu 0.45 - 0.9 - Mg 0 7 - 1.2 - Ti < 0.15 - Zn < 0 4 - Fe < 0.7 - one or more of Zr, Cr, V each < 0.25 - incidental elements and impurities, each < 0.05, total < 0.25, - the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105HB.
- Si 1 4 - 2.1 - Mn 0 8 - 1 2 - Cu 0.45 - 0.9 - Mg 0 7 - 1.2 - Ti < 0.15 - Zn < 0 4 - Fe < 0.7 - one or more of Zr, Cr, V each < 0.25 - incidental elements and impurities, each < 0.05, total < 0.25, - the balance aluminium, and having a thickness of more than 0.6 mm and in T6 temper condition having a hardness of more than 105HB.
2. Moulding plate according to claim 1 wherein Si is in the range of 1.53 -2.0 %, more preferably in the range of 1.55-1.9 %.
3. Moulding plate according to claim 1 or 2 wherein Mn is in the range of 0 85 -1.10%.
4. Moulding plate according to any of the claims 1 to 3 wherein Cu is in the range of 0.5 - 0.7 %.
5. Moulding plate according to any of the claims 1 to 4 wherein Mg is in the range of 0 9 - 1 1 %.
6. Moulding plate according to any of the claims 1 to 5 wherein Zn is below 0 3%, preferably in the range of 0.17 - 0 3 %.
7. Moulding plate according to any one of claims 1 to 6, wherein the moulding plate has a machinability rating of "B" or better.
8. Moulding plate according to any one of claims 1 to 7, wherein the moulding plate has a final thickness in the range of 5 to 300 mm, preferably 5 to 260 mm.
9. Moulding plate according to any one of claims 1 to 8, wherein the moulding plate has been rolled to the final thickness by hot rolling only.
10. Method of manufacturing a moulding plate comprising the subsequent steps of:
.cndot. casting a composition comprising (in weight percent):
~ Si 1 4 - 2.1 ~ Mn 0 8 - 1.2 ~ Cu 0 45 - 0.9 ~ Mg 0 7 - 1 2 ~ Ti < 0.15 ~ Zn < 0.4 ~ Fe < 0 7 ~ one or more of Zr, Cr, V each < 0.25 ~ incidental elements and impurities, each < 0 05, total < 0 25, balance aluminium.
.cndot. homogenising and preheating, .cndot. working said plate to a final thickness, .cndot. subjecting to heat treatment comprising solution heat treating followed by rapid cooling, .cndot. ageing, wherein the cooling rate during said rapid cooling is chosen so as to obtain a hardness of the moulding plate of at least 105 HB.
.cndot. casting a composition comprising (in weight percent):
~ Si 1 4 - 2.1 ~ Mn 0 8 - 1.2 ~ Cu 0 45 - 0.9 ~ Mg 0 7 - 1 2 ~ Ti < 0.15 ~ Zn < 0.4 ~ Fe < 0 7 ~ one or more of Zr, Cr, V each < 0.25 ~ incidental elements and impurities, each < 0 05, total < 0 25, balance aluminium.
.cndot. homogenising and preheating, .cndot. working said plate to a final thickness, .cndot. subjecting to heat treatment comprising solution heat treating followed by rapid cooling, .cndot. ageing, wherein the cooling rate during said rapid cooling is chosen so as to obtain a hardness of the moulding plate of at least 105 HB.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| EP04077718.7 | 2004-10-05 | ||
| EP04077718 | 2004-10-05 | ||
| PCT/EP2005/010805 WO2006037647A1 (en) | 2004-10-05 | 2005-10-04 | High hardness aluminium moulding plate and method for producing said plate |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CA2582249A1 true CA2582249A1 (en) | 2006-04-13 |
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Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CA002582249A Abandoned CA2582249A1 (en) | 2004-10-05 | 2005-10-04 | High hardness aluminium moulding plate and method for producing said plate |
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| Country | Link |
|---|---|
| US (1) | US20060070686A1 (en) |
| EP (1) | EP1802782B1 (en) |
| CN (1) | CN100562595C (en) |
| AT (1) | ATE389736T1 (en) |
| CA (1) | CA2582249A1 (en) |
| DE (2) | DE602005005509T2 (en) |
| ES (1) | ES2302247T3 (en) |
| FR (1) | FR2876117B1 (en) |
| WO (1) | WO2006037647A1 (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| DE102006039684B4 (en) * | 2006-08-24 | 2008-08-07 | Audi Ag | Aluminum safety component |
| US9314826B2 (en) | 2009-01-16 | 2016-04-19 | Aleris Rolled Products Germany Gmbh | Method for the manufacture of an aluminium alloy plate product having low levels of residual stress |
| CN102282284A (en) * | 2009-01-16 | 2011-12-14 | 阿勒里斯铝业科布伦茨有限公司 | Method for the manufacture of an aluminium alloy plate product having low levels of residual stress |
| WO2011042339A1 (en) * | 2009-10-08 | 2011-04-14 | Aleris Aluminum Duffel Bvba | Multilayer tube with an aluminium alloy core tube |
| JP5495183B2 (en) | 2010-03-15 | 2014-05-21 | 日産自動車株式会社 | Aluminum alloy and high strength bolt made of aluminum alloy |
| MX2018008367A (en) * | 2016-01-08 | 2018-12-10 | Arconic Inc | New 6xxx aluminum alloys, and methods of making the same. |
| SI24911A (en) | 2016-03-04 | 2016-07-29 | Impol 2000, d.d. | High-strength aluminum alloy Al-Mg-Si and procedure for its manufacture |
| CN107245614B (en) * | 2017-07-27 | 2019-01-22 | 广州致远新材料科技有限公司 | A kind of wear-resistant aluminum alloy and application thereof |
| CN108300907B (en) * | 2018-02-10 | 2020-07-21 | 沈阳航空航天大学 | Al-Mn-Si-Mg alloy material and preparation method thereof |
| CN109136670B (en) * | 2018-08-21 | 2019-11-26 | 中南大学 | A kind of 6XXX line aluminium alloy and preparation method thereof |
| CN112430766B (en) * | 2020-11-03 | 2022-02-18 | 福建祥鑫股份有限公司 | High-strength low-yield-ratio 6-series aluminum alloy and preparation method thereof |
| JP2022150384A (en) * | 2021-03-26 | 2022-10-07 | 本田技研工業株式会社 | Aluminum alloy, manufacturing method for additive-manufactured article, and additive-manufactured article |
| CN114277268B (en) * | 2021-12-24 | 2023-04-07 | 东北轻合金有限责任公司 | Manufacturing method of aluminum alloy foil for brazing |
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|---|---|---|---|---|
| JPH04325650A (en) * | 1991-04-24 | 1992-11-16 | Kobe Steel Ltd | Aluminum alloy for metal mold and its production |
| JPH04325645A (en) * | 1991-04-25 | 1992-11-16 | Furukawa Alum Co Ltd | Aluminum alloy excellent in strength after baking hardening and its production |
| JPH07197219A (en) * | 1993-12-28 | 1995-08-01 | Furukawa Electric Co Ltd:The | Production of aluminum alloy sheet for forming |
| JP2823797B2 (en) * | 1994-02-16 | 1998-11-11 | 住友軽金属工業株式会社 | Manufacturing method of aluminum alloy sheet for forming |
| US5961752A (en) * | 1994-04-07 | 1999-10-05 | Northwest Aluminum Company | High strength Mg-Si type aluminum alloy |
| FR2726007B1 (en) * | 1994-10-25 | 1996-12-13 | Pechiney Rhenalu | PROCESS FOR PRODUCING ALSIMGCU ALLOY PRODUCTS WITH IMPROVED INTERCRYSTALLINE CORROSION RESISTANCE |
| US6004409A (en) * | 1997-01-24 | 1999-12-21 | Kaiser Aluminum & Chemical Corporation | Production of high quality machinable tolling plate using brazing sheet scrap |
| JP3324093B2 (en) * | 1999-08-25 | 2002-09-17 | 古河電気工業株式会社 | Aluminum alloy material for forging for automotive parts and forged automotive parts |
| FR2807449B1 (en) * | 2000-04-07 | 2002-10-18 | Pechiney Rhenalu | METHOD FOR MANUFACTURING STRUCTURAL ELEMENTS OF ALUMINUM ALLOY AIRCRAFT AL-SI-MG |
| EP1167560B1 (en) * | 2000-06-27 | 2010-04-14 | Corus Aluminium Voerde GmbH | Aluminium casting alloy |
-
2005
- 2005-10-03 US US11/240,629 patent/US20060070686A1/en not_active Abandoned
- 2005-10-04 DE DE602005005509T patent/DE602005005509T2/en not_active Expired - Fee Related
- 2005-10-04 CN CNB2005800339626A patent/CN100562595C/en not_active Expired - Fee Related
- 2005-10-04 AT AT05805867T patent/ATE389736T1/en not_active IP Right Cessation
- 2005-10-04 EP EP05805867A patent/EP1802782B1/en active Active
- 2005-10-04 DE DE102005047406A patent/DE102005047406A1/en not_active Ceased
- 2005-10-04 ES ES05805867T patent/ES2302247T3/en active Active
- 2005-10-04 FR FR0510136A patent/FR2876117B1/en not_active Expired - Fee Related
- 2005-10-04 CA CA002582249A patent/CA2582249A1/en not_active Abandoned
- 2005-10-04 WO PCT/EP2005/010805 patent/WO2006037647A1/en active IP Right Grant
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| WO2006037647A1 (en) | 2006-04-13 |
| CN100562595C (en) | 2009-11-25 |
| FR2876117B1 (en) | 2007-10-26 |
| DE102005047406A1 (en) | 2006-06-01 |
| FR2876117A1 (en) | 2006-04-07 |
| ES2302247T3 (en) | 2008-07-01 |
| DE602005005509T2 (en) | 2009-04-16 |
| US20060070686A1 (en) | 2006-04-06 |
| EP1802782B1 (en) | 2008-03-19 |
| ATE389736T1 (en) | 2008-04-15 |
| CN101035919A (en) | 2007-09-12 |
| DE602005005509D1 (en) | 2008-04-30 |
| EP1802782A1 (en) | 2007-07-04 |
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