EP3505649B1 - Alliage d'aluminium coulé sous pression, procédé de production d'un alliage d'aluminium coulé sous pression et produit de communications - Google Patents

Alliage d'aluminium coulé sous pression, procédé de production d'un alliage d'aluminium coulé sous pression et produit de communications Download PDF

Info

Publication number
EP3505649B1
EP3505649B1 EP18248147.3A EP18248147A EP3505649B1 EP 3505649 B1 EP3505649 B1 EP 3505649B1 EP 18248147 A EP18248147 A EP 18248147A EP 3505649 B1 EP3505649 B1 EP 3505649B1
Authority
EP
European Patent Office
Prior art keywords
die casting
aluminum alloy
casting aluminum
mass percentage
alloy according
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Active
Application number
EP18248147.3A
Other languages
German (de)
English (en)
Other versions
EP3505649A1 (fr
Inventor
Xiaorui Liu
Naier Meng
Banghong Hu
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Huawei Technologies Co Ltd
Original Assignee
Huawei Technologies Co Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Huawei Technologies Co Ltd filed Critical Huawei Technologies Co Ltd
Publication of EP3505649A1 publication Critical patent/EP3505649A1/fr
Application granted granted Critical
Publication of EP3505649B1 publication Critical patent/EP3505649B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • 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
    • C22C21/04—Modified aluminium-silicon alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B22—CASTING; POWDER METALLURGY
    • B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
    • B22D21/00—Casting non-ferrous metals or metallic compounds so far as their metallurgical properties are of importance for the casting procedure; Selection of compositions therefor
    • B22D21/002—Castings of light metals
    • B22D21/007—Castings of light metals with low melting point, e.g. Al 659 degrees C, Mg 650 degrees C
    • 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
    • C22C1/026—Alloys based on aluminium
    • 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
    • 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
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/043—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

Definitions

  • the present invention relates to the field of aluminum alloy material technologies, and in particular, to a die casting aluminum alloy, a production method of the die casting aluminum alloy, and a communications product.
  • a communications product constantly strives for large power, miniaturization, and lightness. Consequently an increasingly high requirement is imposed on a heat dissipation capability of a die casting material of the communications product.
  • a commonly used die casting material of the communications product is mainly a die casting aluminum alloy.
  • common thermal conductivity of a die casting aluminum alloy in the communications product industry is 90 W/(m ⁇ K) to 150 W/(m ⁇ K), and a requirement of a future product with high heat flux density and large power cannot be met.
  • a communications die-casting fitting is usually in a complex structure with a large quantity of complex thin-wall heat sink fins, higher and lower bosses, and deep-cavity structures, and has relatively large dimensions.
  • a heat sink fin layout of a future heat sink is to be denser and thinner, and a fin shape is to be more complex. Therefore, a requirement on casting fluidity of the die casting material of the communications product is to be higher. Fluidity of an aluminum-silicon (Al-Si) series die casting aluminum alloy commonly used in a current industry increases as content of silicon increases, and the fluidity is the best in a eutectic composition, but thermal conductivity of the alloy decreases at the same time.
  • WO 2018 095 186 discloses an Al-Si-Mg alloy that has been developed to provide an alternative alloy to ADC12 for use in electronic applications that has improved heat conduction properties whilst still maintaining high strength.
  • a first aspect of embodiments of the present invention provides a die casting aluminum alloy according to independent claim 1, that has both a high heat-conducting property and good formability, to resolve a prior-art problem that forming and heat dissipation requirements of a communications product with a complex structure, high heat flux density, and large power cannot be met at the same time because it is difficult for a die casting aluminum alloy to have both a high heat-conducting property and good formability.
  • the first aspect of the embodiments of the present invention provides the die casting aluminum alloy, including constituents with the following mass percentages:
  • a mass percentage of the silicon is 5.5% to 6.5%.
  • the mass percentage of the silicon is 5.8% to 6.3%.
  • the mass percentage of the silicon is 5.7%.
  • a mass percentage of the silicon is 4.3% to 5.0%.
  • the mass percentage of the silicon is 4.4% to 4.8%.
  • a mass percentage of the silicon is 6.5% to 7.5%.
  • a mass percentage of the magnesium is 0.3% to 0.8%.
  • the mass percentage of the magnesium is 0.4% to 0.7%.
  • the mass percentage of the magnesium is 0.5% to 0.6%.
  • a mass percentage of the copper is 0.001% to 0.05%.
  • the mass percentage of the copper is 0.01% to 0.03%.
  • a mass percentage of the manganese is 0.001% to 0.006%.
  • the mass percentage of the manganese is 0.002% to 0.004%.
  • a mass percentage of the zinc is 0.001% to 0.02%.
  • the mass percentage of the zinc is 0.001% to 0.008%.
  • the mass percentage of the iron is 0.5% to 0.7%.
  • a mass percentage of the titanium is 0.05% to 0.06%.
  • a total mass percentage of elements other than the aluminum in the die casting aluminum alloy in the present invention is less than 10%.
  • the total mass percentage of the elements other than the aluminum in the die casting aluminum alloy in the present invention is 5.0% to 8.0%.
  • Phases inside an organization structure of the die casting aluminum alloy include a hypoeutectic ⁇ -Al phase, a eutectic ⁇ -Al phase, a eutectic Si phase, and an intermetallic compound, the intermetallic compound is distributed at a grain boundary location or is precipitated in the hypoeutectic ⁇ -Al phase and the eutectic ⁇ -Al phase, and the intermetallic compound includes an Mg 2 Si phase.
  • the constituents of the die casting aluminum alloy further include an element Fe and an element Cu
  • the intermetallic compound further includes an Al 3 Fe phase, an Al 2 Cu phase, and a ternary compound Al-Si-Fe phase.
  • a coefficient of thermal conductivity of the die casting aluminum alloy is 170 W/(m ⁇ K) to 195 W/(m ⁇ K).
  • Brinell hardness of the die casting aluminum alloy is 60 HBW to 80 HBW, tensile strength is 170 MPa to 220 MPa, yield strength is greater than or equal to 100 MPa, and an elongation rate is greater than or equal to 2%.
  • the die casting aluminum alloy provided in the first aspect of the embodiments of the present invention has both a high heat-conducting property and good formability, also has high corrosion resistance, a good mechanical property, and low costs, and can meet forming and heat dissipation requirements of a communications product with a complex structure.
  • a second aspect of the embodiments of the present invention provides a production method of a die casting aluminum alloy, including the following steps: providing raw materials based on constituents of a die casting aluminum alloy, and performing heat treatment at any temperature within 180°C to 375°C after casting, to obtain a die casting aluminum alloy, where the die casting aluminum alloy includes constituents with the following mass percentages: silicon: 4.0% to 10.0%; magnesium: 0.2% to 1.0%; copper: ⁇ 0.1%; manganese: ⁇ 0.1%; zinc: ⁇ 0.1%; iron: 0.5% to ⁇ 1.0%; titanium: 0.05% to 0.2%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • the foregoing heat treatment process may be at a constant temperature, or may be at a non-constant temperature.
  • a temperature may be selected from 180°C to 375°C to perform heat treatment.
  • a plurality of temperatures may be separately selected from 180°C to 375°C as heat treatment temperatures at a plurality of heat treatment stages.
  • the casting is performed through liquid die casting, semi-solid die casting, vacuum die casting, investment casting, gravity casting, or squeeze casting.
  • time for the heat treatment is 0.2h to 8h.
  • a process of the production method provided in the second aspect of the present invention is simple, and the produced die casting aluminum alloy has both a high heat-conducting property and good formability, and also has high corrosion resistance and a good mechanical property.
  • a third aspect of the embodiments of the present invention provides a communications product, including a housing and a power supply circuit and a functional circuit that are located in the housing, where the power supply circuit supplies power to the functional circuit, and the housing is obtained through casting by using the die casting aluminum alloy according to the first aspect of the embodiments of the present invention.
  • the communications product provided in the third aspect of the embodiments of the present invention has a high heat-conducting property, good formability, high corrosion resistance, and a mechanical property, and can meet a design requirement for high density and large power.
  • a communications product constantly strives for large power, miniaturization, and lightness, the industry imposes an increasingly high requirement on a heat dissipation capability of a die casting material of the communications product.
  • a commonly used die casting material of the communications product is mainly a die casting aluminum alloy.
  • common thermal conductivity of a die casting aluminum alloy in the communications product industry is 90 W/(m ⁇ K) to 150 W/(m ⁇ K), and a requirement of a future product with high heat flux density and large power cannot be met.
  • a communications die-casting fitting is usually in a complex structure with a large quantity of complex thin-wall heat sink fins, higher and lower bosses, and deep-cavity structures, and has relatively large dimensions.
  • a heat sink fin layout of a future heat sink is to be denser and thinner, and a fin shape is to be more complex. Therefore, a requirement on casting fluidity of the die casting material of the communications product is to be higher. Fluidity of an Al-Si series die casting aluminum alloy commonly used in a current industry increases as content of silicon increases, and the fluidity is the best in a eutectic composition, but thermal conductivity of the alloy decreases at the same time. Therefore, it is difficult to have both a high heat-conducting property and good formability. In view of this, currently, to develop a die casting aluminum alloy with both a high heat-conducting property and good formability has become an urgent need in the communications industry.
  • the die casting aluminum alloy needs to have both relatively high corrosion resistance and a mechanical property.
  • the present invention provides a die casting aluminum alloy that has both a high heat-conducting property and good formability.
  • the die casting aluminum alloy includes constituents with the following mass percentages:
  • the constituents of the alloy are determined by comprehensively considering contribution of each chemical element to an integrated performance index (including thermal conductivity, fluidity, corrosion resistance, hardness, strength, and the like) of the alloy, and with a joint effect of various elements of the foregoing specific content, different types of performance are balanced, and a stable crystal structure is formed, so that a die casting aluminum alloy with good integrated performance is obtained.
  • an integrated performance index including thermal conductivity, fluidity, corrosion resistance, hardness, strength, and the like
  • Phases inside an organization structure of the die casting aluminum alloy in this embodiment of the present invention include a hypoeutectic ⁇ -Al phase, a eutectic ⁇ -Al phase, a eutectic Si phase, and an intermetallic compound, and the intermetallic compound is distributed at a grain boundary location or is precipitated in the ⁇ -Al phases.
  • the phase means uniform and continuous components having a same chemical composition, a same atom aggregation state, and a same atom property, and different phases are separated by an interface.
  • the intermetallic compound is a compound including a metal and a metal, or a metal and a metalloid.
  • the intermetallic compound mainly includes an Mg 2 Si phase.
  • the constituents of the die casting aluminum alloy further include an element Fe and an element Cu
  • the intermetallic compound further includes an Al 3 Fe phase, an Al 2 Cu phase, a ternary compound Al-Si-Fe phase, and the like.
  • the iron, the copper, the magnesium, the manganese, the zinc, and the titanium are partially solidly dissolved in the hypoeutectic ⁇ -Al phase and the eutectic ⁇ -Al phase in a form of atoms.
  • the Al 2 Cu phase and the Mg 2 Si phase are uniformly dispersed and distributed.
  • Adding of the element silicon (Si) can improve casting fluidity of an Al-Si series alloy, and in the alloy, Si and Al form an ( ⁇ -Al+Si) eutectic phase. This is a main reason why casting fluidity of the aluminum-silicon alloy is improved.
  • thermal conductivity of the alloy decreases as content of Si increases.
  • thermal conductivity of an aluminum alloy with a Japanese designation ADC12 in which content of silicon is 9.6% to 12%) is only 95 W/(m ⁇ K). This is because a large amount of Si in the Al-Si alloy exists mainly in a form of primary Si or eutectic Si or is solidly dissolved in an Al matrix, and consequently the thermal conductivity of the alloy greatly decreases.
  • a mass percentage of the silicon is controlled within 4.0% to 8.0%. Further, in an implementation of the present invention, the mass percentage of the silicon is specifically controlled within 5.5% to 6.5%, and is further 5.8% to 6.3%, or 5.7%, or 6.0%. In another implementation of the present invention, the mass percentage of the silicon is specifically controlled within 4.3% to 5.0%, and is further 4.4% to 4.8%, or 4.5%, or 4.7%. In other implementations of the present invention, the mass percentage of the silicon may alternatively be 6.5% to 7.5%, and is further 7.0%.
  • the element magnesium (Mg) is a main strengthening element in the aluminum-silicon alloy.
  • Mg and Si form the Mg 2 Si phase that is uniformly dispersed and distributed in the organization structure of the alloy and performs a dispersion strengthening function.
  • the dispersion strengthening means a material strengthening effect achieved by organizing and mixing a plurality of phases.
  • the dispersion strengthening is essentially using dispersed ultra-fine particles to hinder dislocation motion, thereby improving a mechanical property of a material at a high temperature.
  • the grain boundary is an interface between grains with a same structure and different orientations, in other words, a contact interface between grains.
  • atom arrangement is in transition from one orientation to another.
  • the atom arrangement is in a transition state at the crystal boundary. Consequently, a heat conduction path loses continuity at the crystal boundary, and finally thermal conductivity of a material decreases. Therefore, in consideration of both the mechanical property and the thermal conductivity, in an implementation of the present invention, a mass percentage of the element Mg is controlled within 0.2% to 1.0%. Further, in an implementation of the present invention, the mass percentage of the magnesium is 0.3% to 0.8%, and is further 0.4% to 0.7% or 0.5% to 0.6%.
  • the element copper (Cu) is also a main strengthening element in the aluminum-silicon alloy.
  • Cu and Al form the Al 2 Cu phase that is uniformly dispersed and distributed in the organization structure of the alloy and performs a dispersion strengthening function.
  • solidly dissolved copper has a high cathode effect on the alloy, a copper ion that enters a liquid corrosion dielectric solution is re-plated on a surface of the aluminum alloy in a state of a fine metallic copper grain, to form activity and even large galvanic corrosion, thereby reducing corrosion resistance of the alloy.
  • the solidly dissolved copper and a metal that is in the alloy and that has different potential from that of the copper form a micro battery when there is the corrosion dielectric solution.
  • the copper acts as a cathode, and another metal with relatively negative potential acts as an anode.
  • the copper ion in the corrosion dielectric solution is reduced to metallic copper and the metallic copper is deposited on a surface of the aluminum alloy, thereby accelerating electrochemical corrosion. Therefore, for obtaining superior corrosion resistance, content of the copper needs to be controlled to control content of solidly dissolved copper, so as to reduce galvanic corrosion.
  • a mass percentage of the element Cu is controlled to be less than or equal to 0.1%.
  • the mass percentage of the copper is 0.001% to 0.05%, and further, the mass percentage of the copper is 0.003% to 0.005%, or 0.008% to 0.01%, or 0.01% to 0.03%, or 0.02% to 0.05%, or 0.03% to 0.04%. In another implementation of the present invention, the mass percentage of the copper is 0.07% to 0.1%, and is further 0.08% to 0.09%.
  • the element iron (Fe) forms a needle-like brittle phase in the die casting aluminum alloy.
  • Existence of the Fe splits a matrix, it is likely to cause stress concentration around the brittle phase, and a fatigue crack or static load fracture occurs on the alloy, thereby reducing a mechanical property of the alloy. Therefore, content of Fe is limited to some extent.
  • excessively low content of Fe leads to an increase in a mold sticking risk during casting, and the element Fe has relatively small impact on thermal conductivity. Therefore, after comprehensive consideration, a mass percentage of the element Fe is controlled to be less than 0.5-1.0% in the present invention. In an implementation of the present invention, the mass percentage of the iron is 0.5% to 0.7%, and is further 0.7% to 0.9%, or 0.8% to 1.0%.
  • Adding of the element manganese (Mn) may improve a mechanical property and corrosion resistance of the aluminum-silicon alloy.
  • Mn has relatively large impact on thermal conductivity at the same time, and reduces a heat-conducting property of the alloy. Therefore, a content range of the element Mn may be specifically determined based on the content of the element Fe, and is specifically controlled to be less than or equal to 0.1% in this embodiment of the present invention.
  • a mass percentage of the manganese is 0.001% to 0.006%, and is further 0.002% to 0.003%.
  • a mass percentage of the manganese may alternatively be 0.004% to 0.005%, or 0.008% to 0.01%, or 0.012% to 0.05%, or 0.04% to 0.06%, or 0.07% to 0.08%.
  • the element titanium (Ti) preferentially reacts with Al to form an Al 3 Ti grain refiner that can convert ⁇ -Al grains from a thick branch shape into fine and uniform equiaxed grains, so that strength and plasticity of the aluminum alloy are improved, but a heat-conducting property of a material is reduced at the same time.
  • the Al 3 Ti grain refiner has an excellent refinement effect, improves surface quality of castings so that the castings obtain fine equiaxed grains, especially reduces casting cold shuts and eliminates a trichite and a columnar crystal, and can effectively overcome casting cracks and improve a casting appearance.
  • the equiaxed grains are grains with a relatively small grain dimension difference in all orientations.
  • a mass percentage of the titanium is controlled to be greater than 0 and less than or equal to 0.2%. Further, in an implementation of the present invention, the mass percentage of the titanium is 0.05% to 0.06%. In other implementations of the present invention, the mass percentage of the titanium may alternatively be 0.07% to 0.08% or 0.1% to 0.15%.
  • a mass percentage of the zinc is specifically 0.001% to 0.02%, and is further 0.001% to 0.008%. In another implementation of the present invention, a mass percentage of the zinc is greater than 0 and less than or equal to 0.001%. In other implementations of the present invention, a mass percentage of the zinc may alternatively be 0.03% to 0.06%, or 0.07% to 0.08%, or 0.09% to 0.1%.
  • content of the inevitable impurity elements is controlled to be less than or equal to 0.15%.
  • the die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.8% to 6.3%; magnesium: 0.3% to 0.4%; copper: ⁇ 0.1%; manganese: ⁇ 0.08%; zinc: ⁇ 0.02%; iron: 0.5% to 0.68%; titanium: >0% and ⁇ 0.02%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • the die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.7%; magnesium: 0.33%; copper: 0.1%; manganese: 0.001%; zinc: ⁇ 0.001%; iron: 0.58%; titanium: ⁇ 0.001%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a total mass percentage of elements other than the aluminum in the die casting aluminum alloy is controlled to be less than 10%, and is further controlled within 5.0% to 8.0%, or within 5.5% to 7.5%, or within 6.0% to 6.5%.
  • a coefficient of thermal conductivity of the die casting aluminum alloy reaches 170 W/(m ⁇ K) to 195 W/(m ⁇ K)
  • Brinell hardness is 60 HBW to 80 HBW
  • tensile strength is 170 MPa to 220 MPa
  • yield strength is greater than or equal to 100 MPa
  • an elongation rate is greater than or equal to 2%.
  • the tensile strength is a critical value at which a metal is in transition from uniform plastic deformation to local-concentrated plastic deformation, and is also a maximum bearing capability of the metal in a case of static stretching.
  • the tensile strength indicates resistance to maximum uniform plastic deformation of a material, and deformation of a tensile sample is uniform and consistent before the tensile sample bears maximum tensile stress. However, after the maximum tensile stress is exceeded, a necking phenomenon starts to occur on the metal, to be specific, concentrated deformation occurs.
  • the yield strength is a yield limit when a yield phenomenon occurs on a metal material, in other words, stress that resists microplastic deformation.
  • the elongation rate is an index for describing plastic performance of a material, and is a percentage of a ratio of total deformation ⁇ L of a gauge section after tensile fracture of a sample to an original gauge length L.
  • the die casting aluminum alloy provided in the present invention has a high heat-conducting property, good formability, high corrosion resistance, and a mechanical property, can be applied to a harsh outdoor environment, can be used for forming complex thin-wall castings (such as a heat sink) to meet a design requirement for high density and large power, and can be specifically used in fields such as a mobile phone, a notebook computer, a communications device industry, an automobile, and civil hardware. More specifically, an embodiment of the present invention provides a communications product, including a housing and a power supply circuit and a functional circuit that are located in the housing, where the power supply circuit supplies power to the functional circuit, and the housing is obtained through casting by using the die casting aluminum alloy provided in the embodiments of the present invention.
  • the communications product may be a heat sink.
  • another component that can use an aluminum alloy part may also be obtained through casting by using the die casting aluminum alloy in the embodiments of the present invention, such as a handle, a maintenance cavity cover, a guide rail, a rotating shaft, and a supporting kit.
  • an embodiment of the present invention further provides a production method of a die casting aluminum alloy, including the following steps:
  • step S10 all the liquid die casting, the semi-solid die casting, the vacuum die casting, the investment casting, the gravity casting, and the squeeze casting are existing conventional processes.
  • Raw materials and process parameters required for each process are not specially limited in the present invention, and only need to be selected and set according to an industry requirement and an actual requirement.
  • a temperature for the heat treatment is 200°C to 300°C or 240°C to 280°C.
  • a heat treatment process may be at a constant temperature, or may be at a non-constant temperature.
  • time for the heat treatment is 0.2h to 8h, and further, the time for the heat treatment is 1h to 5h or 2h to 6h.
  • the heat treatment in the present invention can strengthen the alloy, and can not only improve a mechanical property (such as strength, hardness, and an elongation rate) of the alloy, but also improve physical performance (including density, conductivity, and thermal conductivity) and electrochemical performance (including solid solution potential) of castings.
  • An alloy element more easily leads to reduction in the conductivity and the thermal conductivity of the alloy when existing in a form of a solid solution in comparison with being combined with another element to form an intermetallic compound. Therefore, heat treatment is even needed during production of a high heat-conductive and electricity-conductive component.
  • a point defect of the alloy such as a vacancy or a solidly dissolved atom can be reduced.
  • the vacancy may be transferred from an interior of a material to a surface of the alloy and escapes, thereby reducing lattice distortion of the alloy, and greatly improving thermal conductivity of the alloy without reducing a mechanical property of the alloy.
  • a dispersion strengthening phase (such as Mg 2 Si or Al 2 Cu) is precipitated from a solid solution, thereby reducing content of a solidly dissolved atom, so that strength and electrical conductivity of the alloy are optimized.
  • a dispersion strengthening phase such as Mg 2 Si or Al 2 Cu
  • dispersion strengthening phases Mg 2 Si and Al 2 Cu, and only a very small quantity of the elements exist inside an ⁇ -Al phase in a form of a solidly dissolved atom.
  • Phases inside an organization structure of the die casting aluminum alloy produced in this embodiment of the present invention include a hypoeutectic ⁇ -Al phase, a eutectic ⁇ -Al phase, a eutectic Si phase, and an intermetallic compound, and the intermetallic compound is distributed at a grain boundary location or is precipitated in the ⁇ -Al phase.
  • the intermetallic compound mainly includes an Al 3 Fe phase, an Al 2 Cu phase, an Mg 2 Si phase, a ternary compound Al-Si-Fe phase, and the like.
  • the iron, the copper, the magnesium, the manganese, the zinc, and the titanium are partially solidly dissolved in the hypoeutectic ⁇ -Al phase and the eutectic ⁇ -Al phase in a form of atoms.
  • the Al 2 Cu phase and the Mg 2 Si phase are uniformly dispersed and distributed.
  • a mass percentage of the silicon is specifically controlled within 5.5% to 6.5%, and is further 4.3% to 4.8% or 4.4% to 5.0%. In other implementations of the present invention, a mass percentage of the silicon may alternatively be 4.5% to 5.0%, or 6.0% to 7.0%, or 6.5% to 7.5%.
  • a mass percentage of the magnesium is 0.3% to 0.7%, and is further 0.4% to 0.5% or 0.6% to 0.8%.
  • a mass percentage of the copper is 0.001% to 0.05%. In another implementation of the present invention, a mass percentage of the copper is 0.08% to 0.1%. In other implementations, a mass percentage of the copper may alternatively be 0.003% to 0.005%, or 0.008% to 0.01%, or 0.02% to 0.05%, or 0.04% to 0.06%.
  • a mass percentage of the iron is further 0.5% to 0.7%. In an implementation of the present invention, a mass percentage of the iron may alternatively be 0.7% to 0.9%, or 0.8% to 1.0%.
  • a mass percentage of the manganese is 0.001% to 0.006%, and is further 0.002% to 0.003%. In other implementations of the present invention, a mass percentage of the manganese may alternatively be 0.004% to 0.005%, or 0.008% to 0.01%, or 0.012% to 0.05%, or 0.04% to 0.06%, or 0.07% to 0.08%.
  • a mass percentage of the zinc is specifically 0.001% to 0.008%.
  • a mass percentage of the zinc is greater than 0 and less than or equal to 0.001%.
  • the die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.8% to 6.3%; magnesium: 0.3% to 0.4%; copper: ⁇ 0.1%; manganese: ⁇ 0.08%; zinc: ⁇ 0.02%; iron: 0.5% to 0.68%; titanium: >0% and ⁇ 0.02%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • the die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.7%; magnesium: 0.33%; copper: 0.1%; manganese: 0.001%; zinc: ⁇ 0.001%; iron: 0.58%; titanium: >0% and ⁇ 0.001%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a process of the production method of the die casting aluminum alloy provided in this embodiment of the present invention is simple, and the produced die casting aluminum alloy has a high heat-conducting property, good formability, high corrosion resistance, and a good mechanical property.
  • a die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.8% to 6.3%; magnesium: 0.3% to 0.4%; copper: ⁇ 0.1%; manganese: ⁇ 0.08%; zinc: ⁇ 0.02%; iron: 0.5% to 0.68%; titanium: >0% and ⁇ 0.02%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a production method of a complex thin-wall communications housing that is obtained through die casting by using the die casting aluminum alloy with the constituents in this embodiment includes the following steps: Based on the constituents of the foregoing die casting aluminum alloy, a pure aluminum A00 aluminum ingot (whose purity is 99.7%), a pure magnesium ingot, an AlSi26 intermediate alloy, an AlFe20 intermediate alloy, and the like are used as raw materials, melting, semi-solid slurrying, and semi-solid die casting are performed on the raw materials, and after cooling, 180°C to 375°C heat treatment is performed for 0.2 to 8 hours, to obtain the thin-wall communications housing.
  • a die casting aluminum alloy includes constituents with the following mass percentages: silicon: 5.7%; magnesium: 0.33%; copper: 0.1%; manganese: 0.001%; zinc: ⁇ 0.001%; iron: 0.58%; titanium: >0% and ⁇ 0.001%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a complex thin-wall communications housing is obtained in the manner in Embodiment 1 of the present invention through die casting by using the die casting aluminum alloy with the constituents in this embodiment.
  • a die casting aluminum alloy includes constituents with the following mass percentages: silicon: 4.7%; magnesium: 0.33%; copper: ⁇ 0.1%; manganese: ⁇ 0.05%; zinc: ⁇ 0.01%; iron: 0.58%; titanium: 0.05% to 0.1%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a complex thin-wall communications housing is obtained in the manner in Embodiment 1 of the present invention through die casting by using the die casting aluminum alloy with the constituents in this embodiment.
  • a die casting aluminum alloy includes constituents with the following mass percentages: silicon: 4.5%; magnesium: 0.46%; copper: ⁇ 0.1%; manganese: ⁇ 0.1%; zinc: ⁇ 0.001%; iron: 0.5% to 0.58%; titanium: 0.05% to 0.1%; inevitable impurities: ⁇ 0.15%; and the rest: aluminum.
  • a complex thin-wall communications housing is obtained in the manner in Embodiment 1 of the present invention through die casting by using the die casting aluminum alloy with the constituents in this embodiment.
  • a comparison test is performed on the die casting aluminum alloys in Embodiment 1 to Embodiment 4 of the present invention and an ADC12 alloy in terms of thermal conductivity, formability, and a mechanical property (including hardness, tensile strength, yield strength, and an elongation rate).
  • a result is as follows:
  • a thermal conductivity test is performed on the die casting aluminum alloys in Embodiment 1 to Embodiment 4 of the present invention and the ADC12 alloy, and the thermal conductivity test is performed by using a laser flash method (ASTM E 1461-01). Sample dimensions are ⁇ 12.7 mm ⁇ (2 to 4) mm. For heat, refer to ISO 11357 and ASTM E1269. For density, refer to ISO 1183-1:2004. A thermal conductivity result of each alloy is shown in Table 1. Table 1 Comparison between thermal conductivity of alloys Alloy designation Thermal conductivity (w/m ⁇ k) ADC12 95 Example 1 185 Example 2 190 Embodiment 3 182 Embodiment 4 180
  • the die casting aluminum alloy in the embodiments of the present invention has a better heat-conducting property than that of the ADC12 aluminum alloy, and can meet a heat dissipation requirement of a communications product with a complex structure, high heat flux density, and large power.
  • Die casting is separately performed on three types of alloys: the alloys in Example 1 and Example 2 of the present invention and the ADC12 alloy, to obtain a complex thin-wall communications housing.
  • the alloys in Example 1 and Example 2 of the present invention and the ADC12 alloy, to obtain a complex thin-wall communications housing.
  • formability of the alloy is poor, a short shot defect is likely to occur on a thin-wall heat sink fin.
  • 30 die-casting fittings are continuously produced by using each alloy.
  • Statistical results of maximum physical dimensions of each short shot feature on 25 heat sink fins of the die-casting fittings are shown in Table 2.
  • the maximum physical dimensions (R) are described in three categories: 0.5 mm ⁇ R ⁇ 1.0 mm, or 1.0 mm ⁇ R ⁇ 3 mm, or R>3 mm.
  • a corrosion resistance test is performed on the die casting aluminum alloys in Embodiment 1 to Embodiment 4 of the present invention. Corrosion resistance of the die casting aluminum alloy is compared with that of an existing alloy, and a result is shown in Table 3. The corrosion resistance of the alloy is indicated by using a corrosion rate.
  • a test method for the corrosion rate complies with the standard GB/T19292.4 and the standard GB/T 16545, and sample dimensions are 120 mm ⁇ 100 mm ⁇ 5 mm. For eliminating an edge effect, an edge of a corrosion rate test sample is wrapped with an adhesive tape. After 1440 h of a neutral salt spray test, an average corrosion rate is calculated by using a weight change before and after salt spray. Table 3 Comparison between corrosion rates of alloys Alloy designation Corrosion rate (mg/(dm 2 ⁇ d)) ADC12 34.0 Example 1 4.5 Example 2 4.3 Embodiment 3 5.0 Embodiment 4 4.6
  • Example 1 and Example 2 of the present invention Die casting is separately performed on the alloys in Example 1 and Example 2 of the present invention and the ADC12 alloy, to obtain a complex thin-wall communications housing.
  • a standard tensile mechanical test piece is cut from a product according to a GB/T 228 requirement, and the mechanical property is tested on a tensile testing machine.
  • a result is shown in Table 4.
  • Table 4 Mechanical properties of alloys Alloy designation Tensile strength (MPa) Yield strength (MPa) Elongation rate (%) Hardness (HBW)
  • ADC12 260 ⁇ 100 0.7 92
  • the die casting aluminum alloy obtained in the embodiments of the present invention has both a high heat-conducting property and good formability, and also has high corrosion resistance and a good mechanical property, thereby resolving a prior-art problem that a heat dissipation requirement of a communications product with high heat flux density and large power cannot be met because a heat-conducting property of a die casting aluminum alloy is poor. Therefore, the following problems can be effectively avoided: a low yield rate of die-casting fittings, severe burn-in caused due to heat emission of a product, corrosion in a harsh environment such as a coastal area, assembling difficulties caused by an insufficient mechanical property, or severe deformation in wind load.

Landscapes

  • Chemical & Material Sciences (AREA)
  • Mechanical Engineering (AREA)
  • Engineering & Computer Science (AREA)
  • Organic Chemistry (AREA)
  • Metallurgy (AREA)
  • Materials Engineering (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Cooling Or The Like Of Semiconductors Or Solid State Devices (AREA)
  • Conductive Materials (AREA)
  • Continuous Casting (AREA)
  • Molds, Cores, And Manufacturing Methods Thereof (AREA)

Claims (24)

  1. Alliage d'aluminium pour la coulée sous pression, constitué de constituants dotés des pourcentages en masse suivants :
    silicium : 4,0 % à 10,0 % ;
    magnésium : 0,2 % à 1,0 % ;
    cuivre : ≤ 0,1 % ;
    manganèse : ≤ 0,1 % ;
    zinc : ≤ 0,1 % ;
    fer: 0,5 % à 1,0 % ;
    titane : 0,05 % à 0,2 % ; et
    impuretés inévitables : ≤ 0,15 % ; et le reste : aluminium.
  2. Alliage d'aluminium pour la coulée sous pression selon la revendication 1, un pourcentage en masse du silicium étant de 5,5 % à 6,5 %.
  3. Alliage d'aluminium pour la coulée sous pression selon la revendication 2, le pourcentage en masse du silicium étant de 5,8 % à 6,3 %.
  4. Alliage d'aluminium pour la coulée sous pression selon la revendication 2, le pourcentage en masse du silicium étant de 5,7 %.
  5. Alliage d'aluminium pour la coulée sous pression selon la revendication 1, un pourcentage en masse du silicium étant de 4,3 % à 5,0 %.
  6. Alliage d'aluminium pour la coulée sous pression selon la revendication 5, le pourcentage en masse du silicium étant de 4,4 % à 4,8 %.
  7. Alliage d'aluminium pour la coulée sous pression selon la revendication 1, un pourcentage en masse du silicium étant de 6,5 % à 7,5 %.
  8. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 7, un pourcentage en masse du magnésium étant de 0,3 % à 0,8 %.
  9. Alliage d'aluminium pour la coulée sous pression selon la revendication 8, le pourcentage en masse du magnésium étant de 0,4 % à 0,7 %.
  10. Alliage d'aluminium pour la coulée sous pression selon la revendication 9, le pourcentage en masse du magnésium étant de 0,5 % à 0,6 %.
  11. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 10, un pourcentage en masse du cuivre étant de 0,001 % à 0,05 %.
  12. Alliage d'aluminium pour la coulée sous pression selon la revendication 11, le pourcentage en masse du cuivre étant de 0,01 % à 0,03 %.
  13. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 12, un pourcentage en masse du manganèse étant de 0,001 % à 0,006 %.
  14. Alliage d'aluminium pour la coulée sous pression selon la revendication 13, le pourcentage en masse du manganèse étant de 0,002 % à 0,004 %.
  15. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 14, un pourcentage en masse du zinc étant de 0,001 % à 0,02 %.
  16. Alliage d'aluminium pour la coulée sous pression selon la revendication 15, le pourcentage en masse du zinc étant de 0,001 % à 0,008 %.
  17. Alliage d'aluminium pour la coulée sous pression selon la revendication 1, le pourcentage en masse du fer étant de 0,5 % à 0,7 %.
  18. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 17, un pourcentage en masse du titane étant de 0,05 % à 0,06 %.
  19. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 18, un pourcentage total en masse d'éléments autres que l'aluminium dans l'alliage d'aluminium pour la coulée sous pression étant inférieur à 10 %.
  20. Alliage d'aluminium pour la coulée sous pression selon la revendication 19, le pourcentage total en masse des éléments autres que l'aluminium dans l'alliage d'aluminium pour la coulée sous pression étant de 5,0 % à 8,0 %.
  21. Alliage d'aluminium pour la coulée sous pression selon la revendication 1, des phases à l'intérieur d'une structure organisationnelle de l'alliage d'aluminium pour la coulée sous pression comprenant une phase d'a-Al hypoeutectique, une phase d'a-Al eutectique, une phase de Si eutectique, et un composé intermétallique, le composé intermétallique étant distribué au niveau d'un emplacement de joint de grain ou étant précipité dans la phase d'a-Al hypoeutectique et la phase d'α-Al eutectique, et le composé intermétallique comprenant une phase de Mg2Si.
  22. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 21, un coefficient de conductivité thermique de l'alliage d'aluminium pour la coulée sous pression étant de 170 W/(m·K) à 195 W/(m·K).
  23. Alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 22, la dureté Brinell de l'alliage d'aluminium pour la coulée sous pression étant de 60 HBW à 80 HBW, la résistance en traction étant de 170 MPa à 220 MPa, la limite d'élasticité étant supérieure ou égale à 100 MPa, et un taux d'élongation étant supérieur ou égal à 2 %.
  24. Produit de communications, comprenant un boîtier et un circuit d'alimentation électrique et un circuit fonctionnel qui sont situés dans le boîtier, le circuit d'alimentation électrique fournissant de l'énergie au circuit fonctionnel, et le boîtier étant obtenu par coulée en utilisant l'alliage d'aluminium pour la coulée sous pression selon l'une quelconque des revendications 1 à 23.
EP18248147.3A 2017-12-29 2018-12-28 Alliage d'aluminium coulé sous pression, procédé de production d'un alliage d'aluminium coulé sous pression et produit de communications Active EP3505649B1 (fr)

Applications Claiming Priority (1)

Application Number Priority Date Filing Date Title
CN201711468332.2A CN109988945A (zh) 2017-12-29 2017-12-29 一种压铸铝合金及其制备方法和通讯产品

Publications (2)

Publication Number Publication Date
EP3505649A1 EP3505649A1 (fr) 2019-07-03
EP3505649B1 true EP3505649B1 (fr) 2021-12-08

Family

ID=65010463

Family Applications (1)

Application Number Title Priority Date Filing Date
EP18248147.3A Active EP3505649B1 (fr) 2017-12-29 2018-12-28 Alliage d'aluminium coulé sous pression, procédé de production d'un alliage d'aluminium coulé sous pression et produit de communications

Country Status (3)

Country Link
US (1) US20190203324A1 (fr)
EP (1) EP3505649B1 (fr)
CN (1) CN109988945A (fr)

Families Citing this family (13)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN109609790B (zh) * 2019-01-28 2021-08-13 苏州铭恒金属科技有限公司 一种铝合金及其铸造方法
CN110714144A (zh) * 2019-10-09 2020-01-21 宁波泰意德过滤技术有限公司 一种用于汽车拨叉的高强度压铸铝合金材料及其制备方法
CN114606417B (zh) * 2020-12-04 2023-02-10 比亚迪股份有限公司 Al-Si系压铸铝合金材料及其制备方法、散热件
CN112646993A (zh) * 2020-12-15 2021-04-13 有研工程技术研究院有限公司 一种适用于高固相半固态流变压铸的铝合金材料
CN112522648B (zh) * 2020-12-29 2022-06-07 重庆慧鼎华创信息科技有限公司 一种提高压铸铝合金导热率的工艺方法
KR102553706B1 (ko) * 2021-01-07 2023-07-10 주식회사 에스제이테크 성형성, 내식성, 고열전도도 및 강도가 우수한 알루미늄 다이캐스팅 합금
CN113106303B (zh) * 2021-03-31 2021-12-14 湖南大学 一种利用Zn微合金化及双级时效制度结合来提高ZL114A合金强度的方法
CN113215453A (zh) * 2021-04-09 2021-08-06 华南理工大学 一种抗退火软化的高导热耐腐蚀铸造铝合金及其制备方法
CN113388761A (zh) * 2021-06-07 2021-09-14 北京有色金属与稀土应用研究所 一种电子封装用铝硅合金盖板材料及其制备方法
CN113564429A (zh) * 2021-08-10 2021-10-29 江苏亚太航空科技有限公司 一种细晶粒铝合金块及其制备工艺和应用
CN113862532A (zh) * 2021-09-06 2021-12-31 国网青海省电力公司 管母金具用铝合金及管母金具的制备方法
CN114277288A (zh) * 2021-12-27 2022-04-05 上海交通大学重庆研究院 一种Al-Si-Zn-Mg高导热高强度压铸铝合金及其制备方法
CN115094281B (zh) * 2022-07-08 2023-09-26 长三角先进材料研究院 一种免热处理可烘烤强化的压铸铝硅合金、制备方法及烘烤强化方法

Family Cites Families (10)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5842748A (ja) * 1981-09-08 1983-03-12 Furukawa Alum Co Ltd ダイカスト用アルミニウム合金
JP2003128065A (ja) * 2001-10-17 2003-05-08 Ryobi Ltd アルミ合金ダイカスト製物流パレット
KR20060130658A (ko) * 2004-04-05 2006-12-19 니폰게이긴조쿠가부시키가이샤 열전도성이 우수한 열처리용 알루미늄 합금 주조재 및 그제조 방법
JP5414310B2 (ja) * 2009-03-06 2014-02-12 日産自動車株式会社 自動車強電部品用ヒートシンク、それを用いたヒートシンクユニット及び自動車強電部品用ヒートシンクの製造方法
CN102251157A (zh) * 2010-05-21 2011-11-23 上海晋拓金属制品有限公司 生产减震器支架的铝合金
JP5747103B1 (ja) * 2014-05-02 2015-07-08 株式会社浅沼技研 アルミニウム合金から成る放熱フィン及びその製造方法
CN104630576B (zh) * 2014-12-29 2017-01-11 江苏中色锐毕利实业有限公司 一种导热性能优异的亚共晶铝硅合金及其制备方法与应用
CN108085541B (zh) * 2016-11-23 2020-04-24 比亚迪股份有限公司 一种导热铝合金及其应用
CN106756294A (zh) * 2016-12-20 2017-05-31 重庆顺博铝合金股份有限公司 用于制备手机外壳的铝合金及其制备方法
CN107812918A (zh) * 2017-10-27 2018-03-20 张希波 一种高速列车电控塞拉门铝合金铸件制造方法及铸件

Non-Patent Citations (1)

* Cited by examiner, † Cited by third party
Title
None *

Also Published As

Publication number Publication date
EP3505649A1 (fr) 2019-07-03
CN109988945A (zh) 2019-07-09
US20190203324A1 (en) 2019-07-04

Similar Documents

Publication Publication Date Title
EP3505649B1 (fr) Alliage d'aluminium coulé sous pression, procédé de production d'un alliage d'aluminium coulé sous pression et produit de communications
EP2952598B1 (fr) Alliage d'aluminium coulé sous pression et son procédé de production et produit de communications
US10870905B2 (en) Low-cost high-heat-conduction die-casting magnesium alloy and manufacturing method therefor
CN105296818A (zh) 一种铝合金及其制备方法和应用
WO2018095186A1 (fr) Alliage d'aluminium thermoconducteur et son utilisation
Dang et al. Effect of Sc and Zr on microstructures and mechanical properties of as-cast Al-Mg-Si-Mn alloys
CN110592445B (zh) 720-740MPa冷挤压Al-Zn-Mg-Cu-Ti铝合金及制备方法
CN107829000A (zh) 一种压铸铝合金材料及其制备方法
CN107937768B (zh) 一种挤压铸造铝合金材料及其制备方法
EP4253584A1 (fr) Alliage d'aluminium et élément structural en alliage d'aluminium
EP2468908A2 (fr) Alliage à base d'aluminium à conductivité thermique élevée pour la coulée sous pression
CN108118226B (zh) 一种高导热、耐蚀、耐热压铸镁合金及其制造方法
US20240011130A1 (en) Aluminum alloy, electronic device, and aluminum alloy preparation method
KR20130134302A (ko) 주조성이 우수한 고열전도도 알루미늄 합금
CN105648284A (zh) 一种铝代铜高导合金材料
CN106834806B (zh) 一种耐蚀锌合金及其制备方法
CN112941372B (zh) 一种铝合金及其应用
CN115491558A (zh) 一种压铸镁合金及其制备方法和应用
CN107460378B (zh) 一种Al-Si-Fe-Mg-Cu合金导体材料及其制备方法
WO2015166992A1 (fr) Ailette de radiateur comprenant de l'alliage d'aluminium et procédé de fabrication de cette dernière
CN112575234A (zh) 一种5g手机用高导热高强韧耐腐蚀的铝合金及制造方法
CN113046606A (zh) 铝合金及其制备方法和铝合金结构件
CN114959376B (zh) 压铸铝合金及其制备方法、电子设备结构件和电子设备
US20120269674A1 (en) Magnesium alloy and method of making the same
US20220325386A1 (en) Aluminum alloys

Legal Events

Date Code Title Description
PUAI Public reference made under article 153(3) epc to a published international application that has entered the european phase

Free format text: ORIGINAL CODE: 0009012

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: REQUEST FOR EXAMINATION WAS MADE

17P Request for examination filed

Effective date: 20181228

AK Designated contracting states

Kind code of ref document: A1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

AX Request for extension of the european patent

Extension state: BA ME

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

17Q First examination report despatched

Effective date: 20200310

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: EXAMINATION IS IN PROGRESS

GRAP Despatch of communication of intention to grant a patent

Free format text: ORIGINAL CODE: EPIDOSNIGR1

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: GRANT OF PATENT IS INTENDED

INTG Intention to grant announced

Effective date: 20210623

GRAS Grant fee paid

Free format text: ORIGINAL CODE: EPIDOSNIGR3

GRAA (expected) grant

Free format text: ORIGINAL CODE: 0009210

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: THE PATENT HAS BEEN GRANTED

AK Designated contracting states

Kind code of ref document: B1

Designated state(s): AL AT BE BG CH CY CZ DE DK EE ES FI FR GB GR HR HU IE IS IT LI LT LU LV MC MK MT NL NO PL PT RO RS SE SI SK SM TR

REG Reference to a national code

Ref country code: GB

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: AT

Ref legal event code: REF

Ref document number: 1453821

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211215

Ref country code: CH

Ref legal event code: EP

REG Reference to a national code

Ref country code: DE

Ref legal event code: R096

Ref document number: 602018027831

Country of ref document: DE

REG Reference to a national code

Ref country code: IE

Ref legal event code: FG4D

REG Reference to a national code

Ref country code: NL

Ref legal event code: FP

REG Reference to a national code

Ref country code: SE

Ref legal event code: TRGR

REG Reference to a national code

Ref country code: LT

Ref legal event code: MG9D

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: RS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: LT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: FI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: BG

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220308

REG Reference to a national code

Ref country code: AT

Ref legal event code: MK05

Ref document number: 1453821

Country of ref document: AT

Kind code of ref document: T

Effective date: 20211208

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: NO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220308

Ref country code: LV

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: HR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: GR

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220309

Ref country code: ES

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SM

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: SK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: RO

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: PT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220408

Ref country code: EE

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: CZ

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

REG Reference to a national code

Ref country code: CH

Ref legal event code: PL

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: PL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: AT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

REG Reference to a national code

Ref country code: DE

Ref legal event code: R097

Ref document number: 602018027831

Country of ref document: DE

REG Reference to a national code

Ref country code: BE

Ref legal event code: MM

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MC

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: IS

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20220408

PLBE No opposition filed within time limit

Free format text: ORIGINAL CODE: 0009261

STAA Information on the status of an ep patent application or granted ep patent

Free format text: STATUS: NO OPPOSITION FILED WITHIN TIME LIMIT

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LU

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211228

Ref country code: IE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211228

Ref country code: DK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: AL

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

26N No opposition filed

Effective date: 20220909

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: SI

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

Ref country code: BE

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: LI

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

Ref country code: CH

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20211231

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: IT

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: CY

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: HU

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT; INVALID AB INITIO

Effective date: 20181228

GBPC Gb: european patent ceased through non-payment of renewal fee

Effective date: 20221228

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: GB

Free format text: LAPSE BECAUSE OF NON-PAYMENT OF DUE FEES

Effective date: 20221228

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: NL

Payment date: 20231116

Year of fee payment: 6

PGFP Annual fee paid to national office [announced via postgrant information from national office to epo]

Ref country code: SE

Payment date: 20231110

Year of fee payment: 6

Ref country code: FR

Payment date: 20231108

Year of fee payment: 6

Ref country code: DE

Payment date: 20231031

Year of fee payment: 6

PG25 Lapsed in a contracting state [announced via postgrant information from national office to epo]

Ref country code: MK

Free format text: LAPSE BECAUSE OF FAILURE TO SUBMIT A TRANSLATION OF THE DESCRIPTION OR TO PAY THE FEE WITHIN THE PRESCRIBED TIME-LIMIT

Effective date: 20211208