CN108291278A - Aluminium alloy - Google Patents
Aluminium alloy Download PDFInfo
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- CN108291278A CN108291278A CN201680060527.0A CN201680060527A CN108291278A CN 108291278 A CN108291278 A CN 108291278A CN 201680060527 A CN201680060527 A CN 201680060527A CN 108291278 A CN108291278 A CN 108291278A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
Abstract
The invention discloses with the aluminium alloy formed as follows：The Si of 0.2 1.8 weight %, the Mg of 0.2 1.8 weight %, the Mn of 0.3 2.5 weight %, the Fe of 0.2 1.5 weight %, the Zr of 0.05 0.75 weight %, the Ti of 0.03 0.18 weight %, optionally one or more following elements：The Cr of 0.1 weight % of highest, the Cu of 0.05 weight % of highest, the Zn of 0.2 1.8 weight %, the Er of 0.02 0.5 weight %；And the grain refiner containing Ti and B of optionally 0.01 0.2 weight %；And aluminium and inevitable impurity are as surplus.The alloy is suitable for the component with high thermal stability, is particularly suitable for casting to produce the component for auto industry by extruding, forging or in permanent mold.
Description
Technical field
The present invention relates to the aluminium alloys of the component for the thermal stability with raising.The component made of the alloy
It is characterized in that after being exposed to high fever, still there is high intensity and high rigidity.The present invention aluminium alloy especially suitable for by squeeze,
Forging or in permanent mold casting manufacture aforementioned type component, and suitable for by thermal bonding method further processing by
This component prepared.The invention further relates to the components manufactured by the alloy, and are related to the aluminium alloy for manufacturing
Component is especially used for the purposes of the component of auto industry.
Background technology
It squeezes and molding is to form the most economical two methods of aluminium alloy.
In extruding, design scheme mainly by types of alloys, can be influenced with operating force and direction of exerting pressure and limitation.Pass through
Another important parameter of extrusion forming is press temperature, and the height of the temperature is formed by particular alloy, especially by it to heat
The limitation of the tolerance of application.Since the local heating of alloy may occur in forming process, especially on die entrance side
Edge region may occur part and melt, this can influence the mechanical performance of extruded product.
In high-pressure casting, design limitation is mainly influenced by desired most simple possible part geometry, because
This method needs are realized without using pluggable core.
The quality of extrusion sections depends not only on machine setting and tool design (mould geometry), and mainly depends on
In selected alloy system.In particular, AlMn (Cu) and AlMgSi alloy systems are widely used in extruded product
(F.OSTERMANN：" Anwendungstechnologie Aluminium ", the 3rd edition, the 456-457 pages, Berlin 2014).
In permanent mold process, especially in die casting, chemical composition and microstructure are similarly for relevant with technology application aspect
Later stage component capabilities play a crucial role.
When passing through forging molding, similarly, since strain energy of distortion may (especially in the case where molding rate is excessively high)
Temperature raising can occur.In this case, hot-spot may occur for workpiece, this can generate microstructure and mechanical performance
Adverse effect.Using this moulding process, equally, the influence of composition of alloy is also vital.
Even if if when designing forging using with the relevant design rule of technique, which has limited design schemes.
As described above, in above-mentioned forming method (squeeze, molding, forge), may be designed certainly due to technology or economic cause
It is restricted by degree.
However, being especially in the automotive industry, the component and component group being using increasingly sophisticated, these components and portion
Part group cannot be produced by the moulding process for such as squeezing or molding, or cannot be produced by the process economics.
By further developing suitable joint method, especially welding or solder/solder brazing is greatly expanded by aluminium
The application of component made of alloy, this is because more complicated component and component group can be produced in this way.
Due to thermal bondings techniques such as the welding of this connection generally use or solder/solder brazing, so in these heat
The reliability and its stability of material are vital under the thermal stress conditions occurred in joint technology.Material answers short term thermal
In the case that the tolerance of power takes notice of external heat and in the case where carrying out expected heating to structure (such as in solder/hard
In soldering or welding) it is all critically important.
In general, past, people increasingly focus on the high processing temperature and operation temperature used in high precision part
The exploitation of aluminium alloy with notable elevated temperature strength down.Especially in the automotive industry, in particular, to by involving an exposure to
The method of possible highest temperature handled after intensity and hardness in terms of stability of material there are demands.
In this case, for being suitable for needed for it need not further be heat-treated and can obtain after production process
The demand of the aluminium alloy of the component of mechanical performance increasingly increases.
Similarly, since ever-increasing operation temperature, such as in the engine components of such as piston, thermal stress is increased
Tolerance be also vital.For this application field, in addition to other required performances, as high-wearing feature, low-density,
Except low heat expansion and good castability, advantageous strength characteristics at high temperature is also required.So far, only with having
It could meet these requirements compared with the casting alloy of high Si content and the mixture of Cu.However, since these alloys are easily formed sky
Gas field trash, so they are little suitable for die-casting process.
Term elevated temperature strength is generally understood as meaning the intensity of material at elevated temperatures.Especially 2xxx types alloy
(AlCu) peak in terms of elevated temperature strength is shown.In addition to this, high temperature is realized by increasing the amount of Si, Cu, Ni or Fe
Intensity, however, thus leading to deterioration (F.OSTERMANN, above-mentioned quotation, 300-303 of mechanical performance (such as fracture toughness)
Page).
At a higher temperature, it is not only possible to the irreversible change of microstructure occur, and therefore make intensity irreversibly
It reduces, and it may also happen that the creep process that wherein material or component are slowly plastically deformed.In 3xxx, 5xxx and 6xxx alloy
Alloy (the F.OSTERMANN of system：" Anwendungstechnologie Aluminium ", the 3rd edition, the 300-304 pages, cypress
Woods, 2014) in can find the aluminum material with advantageous croop property.For welding or solder/solder brazing etc.
Joining technique, usually using 4xxx type aluminium alloys.
In general, required mechanical performance, especially high rigidity, are realized by adding copper or zinc into alloy.Separately
Outside, due to hardening effect, these alloys realize the improvement of mechanical performance through heat-treated.Here, forming metastable phase to resist
Dislocation motion when applied force.Alternatively, using Al-Mn alloys.
Alloy can solderability/can brazeability precondition be material solidus temperature be higher than solder liquid phase
Line temperature.In solder brazing, operating temperature is usually 440-600 DEG C；In solder, operating temperature is less than 440 DEG C.
The temperature curve of brazing process significantly affects mechanical performance.When using the temperature of close solidus, this causes
Material softening.Increasing for intensity can only be by the subsequent nature being quickly cooled down or artificial age-hardening using structure come real
It is existing.
Can solder brazing aluminium alloy quantity it is very limited.This is above-mentioned condition as a result, the i.e. solidus temperature of material
It necessarily is greater than the liquidus temperature of brazing metal.Common Al-Mn alloys are not easy to be influenced by heat, but in the processing close to solidus
At a temperature of, they also show the defect in terms of stiffness.
Furthermore it is known that the aluminium alloy for high temperature application includes the alloying element of addition rare earth metal (such as Sc, Er).This
A little rare earth metals form dispersoid (such as Al in aluminum substrate3Er types), it means that improve machine under raised operating temperature
Tool performance.This alloy known to from 2 110 452 A1 of EP, the alloy have high Cu contents (1.0-8.0 weight %) but not
Containing Zn.
Invention content
In view of above-mentioned requirements, the object of the present invention is to provide a kind of aluminium alloys, it is suitable for extruding, forging and in permanent mould
Casting (especially high-pressure casting) in tool, and be easy to casting and have when as-cast condition and short time apply high fever high hard
Degree.In addition, the alloy has good Joint Properties, especially good brazeability and highly corrosion resistant.In addition, described
Alloy is suitable for producing the component of auto industry, the especially component with increased elevated temperature strength.
These purposes by the aluminium alloy and dependent claims according to main claim specify embodiment and
It is realized using the component of the aluminium alloy of present invention manufacture, and the component connects alternately through joint technology, especially heat
Close technique, further processing.
, not only can be in extrudate using the alloy composite of the present invention, but also it can also be in forging and die casting
In high thermal stability is obtained with good hardness number under manufacture state or as-cast condition.Therefore the alloy is especially suitable for life
Production is used for the temperature stress component of auto industry and/or passes through joint method (the especially thermal bonding of such as solder brazing or welding
Technique) it is further processed.(since the thermal stability of alloy increases, extrusion process or other moulding process can be with highers
Process velocity or higher pressure carry out, and in workpiece be not in hot-spot.)
The alloy of the present invention has consisting of：
The Si of 0.2-1.8 weight %
The Mg of 0.2-1.8 weight %
The Mn of 0.3-2.5 weight %
The Fe of 0.2-1.5 weight %
The Zr of 0.05-0.75 weight %
The Ti of 0.03-0.18 weight %.
In addition, the alloy optionally can also contain one or more following elements with ratio shown in following：
The Cr of 0.1 weight % of highest
The Cu of 0.05 weight % of highest
The Zn of 0.2-1.8 weight %
The Er of 0.02-0.5 weight %.
In addition, the alloy can be optionally containing 0.01-0.2 weight % the grain refiner containing Ti and B.The conjunction
The specified composition of gold is unaffected.When preparing the alloy of the aluminium intermediate alloy form containing the composition, it is preferably added to described
Grain refiner.
Surplus is made of aluminium and inevitable impurity.The ratio of these impurity is preferably up to 0.05 weight % (single)
Or 0.15 weight % (total) of highest.
Prevent the solidus of alloy from reducing surprisingly, it has been found that Cu contents are restricted to 0.05 weight % of highest
To 610 DEG C or less.Preferably, Cu contents are limited to 0.03 weight % of highest.
It moreover has been found that by adjusting Mn contents within the scope of 0.3-2.5 weight %, preferably 0.8-1.5 weight %'s
In the range of Mn, the Mn of more preferable 1.2-1.5 weight %, it can be ensured that the high size and intensity under high temperature, therefore during demoulding
Seldom or warpage will not be occurred.In addition, in the case where by casting method, especially die casting is produced, according to the present invention
The Mn contents of use prevent any adherency in mold and ensure release property.
In addition, it has surprisingly been found that by the way that the ratio (being based on weight percent) of iron/manganese is set in 0.5-
In the range of 0.7, in the range of especially 0.6-0.7, the castability of alloy is improved.If the ratio of Fe/Mn is 2:3 (=
0.67) it, is then particularly advantageous.
Preferred silicone content is 0.6-0.8 weight %, especially 0.7 weight %.About Si contents, it was found that by Si/Mg
Ratio be adjusted in the range of 0.9-1.1 that there is advantageous effect to the hardness of alloy and its castability.It is best in order to obtain
Hardness and castability should preferably keep 1:The ratio of 1 Si/Mg.
Preferred zirconium content is 0.08-0.35 weight %, especially 0.1-0.3 weight %.About Zr contents, it was found that such as
The ratio of fruit Ti/Zr is in the range of 0.15-1, and preferably 1:4 (=0.25), then can further increase the thermal stability of alloy
And castability.
Fe contents are 0.2-1.5 weight %, preferably 0.2-1.0 weight %, especially 0.2-0.8 weight %.As described above
(ratio of Fe/Mn) preferably adjusts Fe contents according to Fe contents.
Mg contents are in the range of the Mg of 0.2-1.8 weight %, preferably 0.2-1.2 weight %, especially 0.2-0.9 weight
Measure %, more preferable 0.7 weight %.
(ratio of Si/Mg) as described above preferably sets Mg contents according to Si contents.
Ti contents are in the range of 0.03-0.18 weight %, preferably in the range of 0.05-0.1 weight %.As described above
(ratio of Ti/Zr) preferably sets Ti contents according to Zr contents.
In addition, it has therefore been surprisingly found that by adding erbium (Er), the thermal stability of alloy can be further increased.According to
Thus preferred embodiment, alloy of the invention contain erbium as another alloying element.By adding 0.02-0.5 weight %
Erbium realize desired effect.Preferably, which is in the range of 0.02-0.3 weight %Er.
In addition, it has therefore been surprisingly found that by adding zinc (Zn), the thermal stability of alloy can be further increased.According to
Thus preferred embodiment, alloy of the invention contain zinc as another alloying element.Optional Zn contents are in 0.2-1.8 weights
In the range of amount %Zn；Preferably 0.4-0.8 weight %, especially 0.5-0.7 weight %.According to other embodiment, Zn
Content is in the range of 0.4-1.2 weight %, preferably 0.6-1.2 weight %, especially 1 weight %.
In addition, it has therefore been surprisingly found that thermal stability can be further increased when alloy element Zn and Er is applied in combination.
Particularly, the Zn, preferably 0.4 weight %- of Er the and 0.2-1.8 weight % of 0.02 weight %-0.5 weight % are added by combination
The Zn of 0.8 weight %, may be implemented this raising.
Preferably, crystal grain refinement is carried out to the alloy of the present invention, wherein using the grain refiner containing Ti and B.In this hair
The ratio of grain refiner in bright alloy is preferably 0.5-2kg/t, more preferably 1.5kg/t.
Preferably, contain Ti and B (surpluses：Aluminium) and during alloy production with preferred 0.5-2kg/t, particularly preferably
The aluminium intermediate alloy of the ratio addition of 1.5kg/t is used as grain refiner.In the Al intermediate alloys, Ti and B substantially with
Crystal or particle form are by comprising may be used as the nuclei of crystallization (such as Τ i Β 2, Α l3 Τ i, Α l Τ i5 Β 1, Α l Τ i6).
Preferably, the intermediate alloy include the Ti of 2.7-3.2 weight %, the especially Ti of 2.9-3.1 weight % and
The B of 0.6-1.1 weight %, the especially B of 0.8-0.9 weight %, in each case, aluminium is surplus.
In addition, the weight ratio of Ti/B is preferably 2.5-3.5 in the intermediate alloy, especially 3:1 (=3.0).
The aluminium alloy of the present invention and the component being produced from it are characterized in that they have at least 55HBW5/250, preferably extremely
Few 65HBW5/250, the more preferably at least Brinell hardness of 80HBW5/250.
The aluminium alloy of the present invention and the component being made from it are further characterized by, solidus temperature >=610 DEG C, especially
It is >=630 DEG C.
It can be optionally subjected to be heat-treated according to application or demand characteristic, alloy of the invention.The heat treatment preferably exists
2-42 hours, especially 6-24 hours periods are carried out at a temperature in the range of 325-425 DEG C, especially 350-400 DEG C.With
After carry out air cooling, or by heat treated alloy in suitable gas (such as air or inert gas) or liquid medium
Quenching in (such as water or oil).Preferred heat treatment is to handle 6-24 hours at 350-400 DEG C, then air cooling.
The alloy of the present invention can be used for manufacturing the component for different application, the application being preferred in auto industry.
The present invention alloy, the alloy being especially heat-treated (seeing above) be suitable for production be subjected to High Operating Temperature (such as up to 250
DEG C or up to 300 DEG C) component (for example, engine components or speed change box part, such as piston, cylinder head, engine cylinder body, change
Fast tank shell, heat exchanger).
In addition, the alloy of the present invention is especially suitable for (especially hard by thermal bonding method, such as solder/solder brazing
Soldering) or welding, the component being further processed.The alloy of the present invention is suitable for for example auto industry and HVAC technologies
Solder/solder brazing is carried out to aluminium parts using fluxing agent, and for the technique in solder/solder brazing stove；Especially use
In manufacture heat exchanger.
Therefore, the present invention expands to the component prepared by the alloy that more in detail above defines.Preferably, by permanent
It is cast in mold, these components is manufactured especially by compression casting, or by squeezing or by forging.It when necessary, can be with
By other methods, especially thermal bonding method (such as solder/solder brazing, welding) or portion is further processed by forging
Part, to obtain complex assemblies or component with complex geometric shapes.
Usually, if it is desired, can be further increased by the alloy system of the present invention by carrying out artificial ageing to component
At component heat resistance.In addition, the increase of Brinell hardness may be implemented by this heat treatment.
It is surprising that it has been found that can be by 150-240 DEG C, preferably 180-220 DEG C, particularly preferred 200 DEG C
Lower to carry out -72 hours 4 hours, preferably 8-24 hours, more preferable 8-12 hours of heat treatment further increased under production conditions
The high rigidity (in general, in the range of 5/250 50-70HBW) of the component manufactured with alloy of the present invention.After the heat treatment,
Component has increased Brinell figure (HBW5/250), generally corresponds to 1.1-1.5 times of initial value (before heat treatment).Even
Hardness can further be improved.
By being heat-treated as described above, can obtain has at least 70, preferably at least 80 Brinell hardness
(HBW5/250) component.Preferably, the component so prepared has within the scope of 70-120, especially in the range of 75-95
Interior Brinell hardness.
The alloy of the present invention and the component feature produced by it are there is high fever long-time exposure at high temperature
Stability.As a result, under such temperature condition, mechanical performance, especially hardness are basicly stable.
Under the influence of high temperature, the component made of the alloy of the present invention varies with temperature aspect in hardness (Brinell hardness) and leads to
Often show following behaviors：
Component is at 150-240 DEG C, preferably 180-220 DEG C, heat exposure -72 hours 4 hours at particularly preferred 200 DEG C, preferably
8-24 hours, more preferable 8-12 hours of the period typically resulted in hardness increase.Due to this increase, component, which has, to be equivalent to
At least 1.1-1.5 times of the Brinell figure of initial Brinell figure (HBW5/250).Even if extending heat treatment (such as more than 3 days, is up to 30
It, even more long), will not have an adverse effect to the hardness of component or other mechanical performances, extension heat treatment for example may be used
Can during use or under the use condition of component it occur in component.
If carried out for a long time at above-mentioned specified temperature heat exposure (>3 days, especially 4 day, even more long, such as
30 days), then show at least 1-1.3 times of the Brinell hardness for being equivalent to initial Brinell figure (HBW5/250) after component.It is preferred that
Ground, even if extension application is hot at the temperature disclosed above (3 days or more long, especially 4 days or more long, such as 30 days), hardness will not
It reduces.Unless reaching hardness increase as described above, initial hardness performance is otherwise at least kept substantially.
Component is at 260-350 DEG C, preferably 280-320 DEG C, heat exposure -72 hours 4 hours at particularly preferred 300 DEG C, preferably
8-24 hours, more preferable 8-12 hours of the period will result only in hardness and slightly decline.In general, after the heat treatment, Bu Shi
Hardness is still up to the 80-95% of initial value (namely based on manufacture state).Preferably, apply even if extending at the temperature disclosed above
Heat (3 days or more long, especially 4 days or more long, such as up to 30 days), Brinell hardness will not occur further change (that is,
Hardness is held essentially constant the about 80-95% in initial value).
Another important and advantageous property of the alloy of the present invention, which is the component thus produced, to be briefly exposed to
Close to the temperature of solidus, the notable deterioration without thus leading to hardness or other mechanical performances.Because such as being connect by heat
When conjunction method (especially solder brazing or welding) further processing, component is exposed to this thermic load, therefore this thermal stability
With actual importance.
The component prepared using the alloy of the present invention can briefly (≤30 minutes, preferably≤20 minute, especially≤15
Minute) it is subjected to the temperature of 400-650 DEG C, preferably 400-620 DEG C, especially 400-610 DEG C, without thus leading to its mechanicalness
Energy, the especially associated degradation of its hardness.After being exposed to heat as described above, only observe that hardness slightly declines.In general, exist
After heat exposure of short duration in this way, Brinell hardness still reaches the 70-95% (manufacture state) of initial value.
Therefore the alloy of the present invention and the component being made from it meet above-mentioned requirements, when in particular to being exposed to high fever
Thermal stability.
The aluminium alloy of the present invention is suitable for manufacturing the portion for auto industry by compression casting, forging or extruding first
Part further adds wherein the component can be further processed optionally by joint technology especially by thermal bonding technique
Work.
The present invention aluminium alloy can be preferred for production during manufacture, further processing or then use when be subjected to carrying
The component of high temperature requirement, such as engine or speed change box part (such as piston, cylinder head, engine cylinder body, transmission housing
Body etc.), heat exchanger and vehicle chassis component and car body component.
The present invention aluminium alloy can prepare by methods known to those skilled in the art, usually by prepare have pair
It should be in the melt of the composition of the above-mentioned alloy composite of the present invention.As described above, alloying element Ti and B are preferably in alloy production mistake
It is added in the form of intermediate alloy in journey.
It is preferable to use continuous vertical casting methods to prepare for the alloy of the present invention.By being carried out in advance to melt with inert gas
Gas treatment, it is ensured that enough melt qualities and the poor hydrogen cast article of production；This be also when exposed to heat obtain high rigidity it is steady
Qualitative important prerequisite condition.Method with inert gas treatment metal bath is as known in the art.
According to preferred embodiment, alloy is subjected to optional heat treatment after its preparation.The heat treatment preferably exists
2-42 hours, especially 6-24 hours periods are carried out at a temperature in the range of 325-425 DEG C, especially 350-400 DEG C.With
After carry out air cooling, or by heat treated alloy in suitable gas (such as air or inert gas) or liquid medium
Quenching in (such as water or oil).Preferred heat treatment is carried out 6-24 hours at 350-400 DEG C, and air cooling is then carried out.
, can also be by known method using the alloy of the present invention, preferably by squeezing, in permanent mold, casting is (special
It is not die casting) and/or forging manufacture component.Optionally, component can by joint method (especially solder brazing or welding) or
It is further processed by moulding process.
According to a preferred embodiment, in order to increase the hardness of component, by the present invention alloy manufacture component into
The heat treatment (artificial ageing) of line option.The heat treatment is at 150-240 DEG C, preferably 180-220 DEG C, at particularly preferred 200 DEG C into
Row -72 hours 4 hours, preferably 8-24 hours, more preferable 8-12 hours of the period.
Specific implementation mode
Embodiment
As starting point or comparative alloy, and commodity in use entitled " Aluman 16 " (AlMn1,6；By Aluminium
Rheinfelden GmbH manufacture) the Al-Mn alloys based on EN AW-3103.This alloy can be hard since solidification point is high
Soldering, it is suitable for die-casting processes.The alloy is for manufacturing cooler and being used for food industry.
Table 1 (following) (the first row, " V ") gives the composition of the alloy.
Due to its relatively high Mn and Fe content, which is characterized in that thering is good thermal stability at high temperature.
However, with above-mentioned new application field (the especially application of auto industry), this alloy has had reached its limit.Especially
It is that hardness is insufficient for required component capabilities.Here, may be implemented significantly by using alloy described in this application
Improve, shown in the test result provided in table 2,3 and 4 as shown below.
Table 1：Composition of alloy
* it is heat-treated according to claim 18
All values are indicated with weight %；Surplus：Aluminium and inevitable impurity.By L1, L2, L3, L4, L5, L6 and L7 table
The row shown is related to different-alloy according to the present invention.L8 corresponds to the L7 being in addition heat-treated according to claim 18, and same
Constitute the alloy of the present invention.
The seven kinds of alloys for the present invention that composition is listed in Table 1 below are prepared by melting：L1, L2, L3, L4, L5, L6 and L7.L8
Corresponding to the L7 being in addition heat-treated according to claim 18.Melting comparative alloy V (" Aluman-16 ", see above) is as ginseng
According to composition is also shown in table 1.With all eight kinds of alloys cast cylinder test body (Height 30mm).
Influence for test temperature to firmness change applies the test sample casting cast by eight kinds of alloys different
Heat.
It is tested at three temperature of different durations.Result is provided in following table 2, table 3 and table 4.
It is tested under 200 DEG C (tables 2) and 300 DEG C (tables 3), is carried out 10 hours and 100 hours under each situation for a long time
Period.
In addition, in order to simulate thermic load and behavior of the alloy in thermal bonding process, carried out at 600 DEG C lasting 900 seconds
The short-term test (table 4) of (15 minutes).
After heat treatment, the test sample handled under specific temperature conditions is cooled to room temperature (about 25 DEG C) in air,
Then Brinell hardness test (HBW5/250 is carried out；Talide test ball；Bulb diameter 5mm).The hardness number of measurement
Arithmetic mean of instantaneous value is listed in table 2,3 and 4.
The result shows that no matter the time length of heat exposure, all aluminium alloys of the invention (L1 to L8) all have than comparison
The higher hardness of alloy V.
It has been found that being in as-cast condition (that is, before test), compared with comparative alloy V, difference of the invention
Alloy (L1 to L8) shows considerably higher hardness.In the case of being heat-treated (10h) at 200 DEG C, it might even be possible to further
Increase hardness (being shown in Table 2).
The different-alloy (L1 to L8) of the every other test display present invention is better than comparative alloy in terms of hardness number.Really
It is real, at a higher temperature or in the longer testing time, compared with as-cast condition, observe that hardness declines (being shown in Table 3 and 4),
But thus obtained hardness number remains above the hardness number of comparative alloy.
Even if the short-term test carried out at 600 DEG C also shows that apparent result.The aluminium alloy L1 to L8 of the present invention is surveyed
The hardness number obtained is compared with the hardness number of comparative alloy V beyond more than 10 Brinell hardness units.
Table 2：Hardness at 200 DEG C compares (HBW5/250)
Table 3：Hardness at 300 DEG C compares (HBW5/250)
Table 4：Hardness at 600 DEG C compares (HBW5/250)
Claims (24)
1. a kind of aluminium alloy is used for the component with the thermal stability improved, it is especially useful in by extruding, forging or permanent
It is cast in mold to produce the component, the alloy has consisting of：
The Si of 0.2-1.8 weight %
The Mg of 0.2-1.8 weight %
The Mn of 0.3-2.5 weight %
The Fe of 0.2-1.5 weight %
The Zr of 0.05-0.75 weight %
The Ti of 0.03-0.18 weight %,
Optionally one or more following elements：
The Cr of 0.1 weight % of highest,
The Cu of 0.05 weight % of highest,
The Zn of 0.2-1.8 weight %,
The Er of 0.02-0.5 weight %；
And the grain refiner containing Ti and B of optionally 0.01-0.2 weight %；
Surplus is aluminium and inevitable impurity.
2. aluminium alloy according to claim 1,It is characterized in that,Mn contents are 0.8-1.5 weight %, preferably 1.2-
1.5 weight %.
3. aluminium alloy according to claim 1 or 2,It is characterized in that,The ratio of Fe/Mn is excellent in the range of 0.5-0.7
It is selected as 2:3.
4. according to preceding claims any one of them aluminium alloy,It is characterized in that,Si contents are 0.6-0.8 weight %, excellent
It is selected as 0.7 weight %.
5. according to preceding claims any one of them aluminium alloy,It is characterized in that,Model of the ratio of Mg/Si in 0.9-1.1
In enclosing, preferably 1:1.
6. according to preceding claims any one of them aluminium alloy,It is characterized in that,Zr contents are 0.08-0.35 weight %,
Preferably 0.1-0.3 weight %.
7. according to preceding claims any one of them aluminium alloy,It is characterized in that,Range of the ratio of Ti/Zr in 0.15-1
It is interior, preferably 1:4.
8. according to preceding claims any one of them aluminium alloy,It is characterized in that,It is to be no more than 0.05 weight %, preferably
Amount no more than 0.03 weight % includes Cu.
9. according to preceding claims any one of them aluminium alloy,It is characterized in that,It is to be no more than 0.1 weight %, preferably
Amount no more than 0.08 weight % includes Cr.
10. according to preceding claims any one of them aluminium alloy,It is characterized in that,It includes 0.02-0.5 weight %'s
Er, the preferably Er of 0.02-0.3 weight %.
11. according to preceding claims any one of them aluminium alloy,It is characterized in that,Zn contents are 0.4-0.8 weight %, excellent
It is selected as 0.5-0.7 weight %.
12. the aluminium alloy according to any of claims 1 to 10,It is characterized in that,Zn contents are 0.4-1.2 weight %,
Preferably 0.6-1.2 weight %, especially 1 weight %.
13. according to preceding claims any one of them aluminium alloy,It is characterized in that,Using including 2.7-3.2 weight %'s
The B of Ti the and 0.6-1.1 weight % of Ti, preferably 2.9-3.1 weight %, the preferably aluminium intermediate alloy of the B of 0.8-0.9 weight %
As grain refiner.
14. aluminium alloy according to claim 13,It is characterized in that,The weight ratio of Ti/B is 2.5- in the intermediate alloy
3.5, preferably 3:1.
15. according to preceding claims any one of them aluminium alloy,It is characterized in that,During the alloy manufactures, to institute
The grain refiner that aluminium intermediate alloy form is added in alloy is stated, the intermediate alloy includes the Ti of 2.7-3.2 weight %, preferably
The B of the Ti and 0.6-1.1 weight % of 2.9-3.1 weight %, the preferably B of 0.8-0.9 weight %, wherein the intermediate alloy table
Reveal 3:1 Ti/B weight ratios, and ratio of the intermediate alloy in the aluminium alloy is 0.5-2kg/t, preferably
1.5kg/t。
16. according to preceding claims any one of them aluminium alloy,It is characterized in that,It has at least 55, preferably at least 65,
More preferably at least 80 Brinell hardness (HBW5/250).
17. according to preceding claims any one of them aluminium alloy,It is characterized in that,Its solidus temperature >=610 DEG C.
18. according to preceding claims any one of them aluminium alloy,It is characterized in that,It is at 325-425 DEG C, preferably 350-
It is heat-treated at 400 DEG C 2-42 hours, it is preferably 6-24 hours, then cooling in gas or liquid medium.
19. a kind of component is especially used for the component of auto industry, by according to preceding claims any one of them alloy
It is made.
20. component according to claim 19,It is characterized in that,Its by being cast in permanent mold, especially by
Die casting, or manufactured by forging, or by squeezing.
21. the component according to claim 19 or 20,It is characterized in that,It is at 150-250 DEG C, at preferably 180-220 DEG C
Experience -72 hours 4 hours, heat treatment in preferably 8-24 hours.
22. component according to claim 21,It is characterized in that,It has within the scope of 70-120, especially in 75-95
Brinell hardness (HBW5/250) in range.
23. according to claim 19 to 22 any one of them component,It is characterized in that,It passes through one or more thermal bondings
Technique is preferably further processed by solder/solder brazing or welding.
24. being used to manufacture for vapour by die casting, forging or extruding according to claim 1 to 18 any one of them aluminium alloy
The purposes of the component of turner industry, wherein the component is further especially by thermal bonding technique optionally by joint technology
Processing.
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| Application Number | Priority Date | Filing Date | Title |
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| DE102015013540.6 | 2015-10-19 | ||
| DE102015013540.6A DE102015013540A1 (en) | 2015-10-19 | 2015-10-19 | aluminum alloy |
| PCT/EP2016/001701 WO2017067647A1 (en) | 2015-10-19 | 2016-10-13 | Aluminum alloy |
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| US (1) | US20180298471A1 (en) |
| EP (1) | EP3365472B1 (en) |
| JP (1) | JP2018534435A (en) |
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| CN113373347A (en) * | 2021-05-28 | 2021-09-10 | 江苏大学 | High-strength, high-toughness, high-heat-conductivity and easy-welding aluminum-based composite material for 5G base station and preparation method thereof |
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| WO2017067647A1 (en) | 2017-04-27 |
| JP2018534435A (en) | 2018-11-22 |
| EP3365472B1 (en) | 2019-06-19 |
| US20180298471A1 (en) | 2018-10-18 |
| MX2018004784A (en) | 2018-08-15 |
| EP3365472A1 (en) | 2018-08-29 |
| ES2745051T3 (en) | 2020-02-27 |
| DE102015013540A1 (en) | 2017-04-20 |
| CA3001925A1 (en) | 2017-04-27 |
| AU2016343539A1 (en) | 2018-05-10 |
| SG11201802535UA (en) | 2018-04-27 |
| ZA201801799B (en) | 2020-09-30 |
| KR20180066231A (en) | 2018-06-18 |
| RU2689825C1 (en) | 2019-05-29 |
| BR112018006057A2 (en) | 2018-10-09 |
| PL3365472T3 (en) | 2019-12-31 |
| IL258749A (en) | 2018-06-28 |
| UA119515C2 (en) | 2019-06-25 |
| SI3365472T1 (en) | 2019-10-30 |
| AU2016343539B2 (en) | 2019-10-24 |
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