CN114540670A - Aluminum alloy for forging and preparation method thereof - Google Patents
Aluminum alloy for forging and preparation method thereof Download PDFInfo
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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
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
- B21J5/00—Methods for forging, hammering, or pressing; Special equipment or accessories therefor
- B21J5/002—Hybrid process, e.g. forging following casting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D11/00—Continuous casting of metals, i.e. casting in indefinite lengths
- B22D11/001—Continuous casting of metals, i.e. casting in indefinite lengths of specific alloys
- B22D11/003—Aluminium alloys
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- 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
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- 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
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- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
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- 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
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- 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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- 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
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- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02T—CLIMATE CHANGE MITIGATION TECHNOLOGIES RELATED TO TRANSPORTATION
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Abstract
The invention discloses an aluminum alloy for forging and a preparation method thereof, wherein the aluminum alloy comprises the following components in percentage by mass: mg: 0.7-1.0%, Si: 1.0-1.7%, Cu: 0.35-0.5%, Mn: 0.55-0.8%, Cr: 0.2 to 0.32%, Zr: 0.05-0.1%, Er: 0.05-015%, Ti: 0.02-0.05%, Fe is less than or equal to 0.25%, the total amount of inevitable impurities is less than or equal to 0.15%, and the balance is Al. The preparation method comprises the steps of preparing the aluminum alloy ingot, carrying out three-stage homogenization treatment, cooling, forging, solid solution, quenching, peak aging treatment and the like. The alloy provided by the invention belongs to Al-Mg-Si-Cu alloy, and the preparation method enables the alloy to have the tensile strength of 420-440MPa and the fatigue strength of 135MPa (N is 1 multiplied by 10) by optimizing alloy components, homogenizing process and peak aging process7) And an excellent value of elongation of not less than 12%. The high-strength anti-fatigue aluminum alloy material provided by the invention is suitable for producing forged parts in the fields of traffic, aviation and the like, for example, a 22.5-inch commercial vehicle high-strength ultra-light forged hub, and has the advantages of reducing weight by 2.5kg compared with a domestic hub with the same specification and reducing weight by 1kg compared with a U.S. hub, prolonging the service time by 1 year and reducing the production cost by 7%.
Description
Technical Field
The invention relates to a non-ferrous metal material, in particular to an aluminum alloy for forging and a preparation method thereof.
Background
With the development of society, people put forward higher requirements on factors such as environmental protection and energy conservation, and the like, so that the lightweight development of automobiles is promoted while the safety performance of the automobiles is improved. The high-quality aluminum alloy forging replaces the original steel part or the aluminum alloy forging with common performance in the automobile field, and is the main target of automobile light weight, such as: commercial car forges aluminum alloy wheel hub and replaces steel wheel hub, passenger car chassis aluminum alloy forges control arm and replaces steel stamping workpiece. The traditional forging material for the automobile is 6061 aluminum alloy, and the product has yield strength of 280MPa, tensile strength of 320MPa and elongation of 10-12%. However, with the progress of weight reduction and the development of forging technology, automobile parts are further required to have long service life, higher stability, further weight reduction and easy forming, so as to realize double improvement and improvement of economy and environment.
The hub serving as a main bearing part of the automobile plays a decisive role in the safety, comfort and stability of the automobile. During the running process, the hub is subjected to the action of various alternating loads, and the action of the loads is easy to generate fatigue cracks and even fatigue failure, so that the improvement of the fatigue performance and the increase of the fatigue life of the hub are necessary prerequisites for the wide application of the aluminum alloy forged hub. The fatigue strength of the traditional forged 6061 aluminum alloy wheel hub which is applied to passenger cars is about 115MPa-120 MPa; the load borne by the hub of the commercial vehicle is larger, the requirement on the fatigue performance of the material is higher, but the annual output of the forged alloy hub is about 400 thousands of wheels when the forged alloy hub is applied to the commercial vehicle. In addition, the existing advanced closed backward extrusion forging process can realize one-step forming of large-size forged parts for automobiles, reduces forming procedures and saves cost. Because the one-step forming strain of the material is far larger than that of the currently adopted two-forging one-rotation process, the traditional 6061 aluminum alloy is difficult to meet the requirement of the advanced forging process on the elongation of the material, and the product yield is low. Accordingly, there is a need for an aluminum alloy material for forging having high elongation and high fatigue strength, which satisfies the requirements of high toughness, long life, light weight, and easy hub forming.
Compared with the American hub, the forged hub of the domestic commercial vehicle has low strength, heavy weight and short service life. Lack of international competitiveness and are difficult to be introduced into the high-end hub market. Therefore, in order to meet the requirements of automobile safety and an advanced forging process on material performance, improve the strength of the hub, reduce the weight of the hub, prolong the service life of the hub, realize the domestic high-strength ultra-light forged hub and exceed the American hub representing the international advanced level, the high-strength anti-fatigue aluminum alloy with strength and fatigue performance far superior to 6061 aluminum alloy is required to be provided.
Disclosure of Invention
Aiming at the problems in the prior art, the invention provides an aluminum alloy for forging and a preparation method thereof, which specifically comprise the following steps:
an aluminum alloy for forging comprises the following components in percentage by mass: mg: 0.7-1.0%, Si: 1.0-1.7%, Cu: 0.35-0.5%, Mn: 0.55-0.8%, Cr: 0.2 to 0.32%, Zr: 0.05-0.1%, Er: 0.05-0.15%, Ti: 0.02-0.05%, Fe is less than or equal to 0.25%, the total amount of inevitable impurities is less than or equal to 0.15%, and the balance is Al.
Specifically, the alloy Mg/Si mass ratio is 0.5 to 1.2, the excess Si amount X is 0.7 to 1.3 wt%, the Mn/X mass ratio is 0.1 to 0.8, the Cr/X mass ratio is 0.1 to 0.5, and the excess Si amount X is for forming Mg2The content of Si remaining after the Si phase.
Specifically, the excess Si includes micron-sized alpha-Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3Si phase, nano AlMnCrSi phase dispersed and precipitated in the homogenization process, and Si solid-dissolved in the matrix.
A preparation method of an aluminum alloy for forging comprises the following steps:
(1) preparing an aluminum alloy ingot: preparing an aluminum alloy ingot by adopting a semi-continuous casting method, wherein the aluminum alloy ingot comprises the following components in percentage by mass: mg: 0.7-1.0%, Si: 1.0-1.7%, Cu: 0.35-0.5%, Mn: 0.55-0.8%, Cr: 0.2 to 0.32%, Zr: 0.05-0.1%, Er: 0.05-0.15%, Ti: 0.02-0.05%, Fe is less than or equal to 0.25%, the total amount of inevitable impurities is less than or equal to 0.15%, and the balance is Al;
(2) three-stage homogenization treatment: sequentially preserving the aluminum alloy ingots obtained in the step (1) at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃, 570 ℃ for 8-12h, 6-10h and 5-11h respectively;
(3) and (3) cooling: air cooling or air cooling the aluminum alloy ingot after the three-stage homogenization treatment;
(4) forging: forging the aluminum alloy ingot obtained in the step (3);
(5) solid solution: carrying out solution treatment on the forged aluminum alloy material;
(6) quenching: quenching the aluminum alloy material after solid solution;
(7) and (3) peak aging treatment: and carrying out peak aging treatment on the quenched aluminum alloy material.
Specifically, the method for preparing the aluminum alloy ingot by the semi-continuous casting method in the step (1) comprises the following steps: the casting speed is 40mm/min-130mm/min, the casting temperature is 680 ℃ to 710 ℃, and the cooling water flow is 2m3/h-20m3The diameter of the alloy ingot is phi 150 mm-phi 350 mm.
Specifically, the forging method in the step (4) is as follows: preserving the heat of the homogenized aluminum alloy ingot for 3 hours at the temperature of 450-510 ℃, and then performing finish forging at the temperature of 400-450 ℃, wherein the forging speed is 6-20 mm/s, and the strain is not lower than 0.5.
Specifically, the solid solution method in the step (5) comprises the following steps: the forged aluminum alloy material is subjected to solution treatment for 2 to 3 hours at the temperature of 520 to 570 ℃.
Specifically, the method for peak aging treatment in the step (7) comprises the following steps: and (3) preserving the heat of the quenched aluminum alloy material for 5-8h at 160-190 ℃.
Specifically, the method further comprises the step (8): and (4) processing the aluminum alloy material obtained after the peak aging treatment into an aluminum alloy product.
The invention has the beneficial effects that:
according to the invention, the trace component Er is added, and the peritectic reaction is generated in the casting process, so that the effect of refining as-cast structure grains is achieved. Simultaneously, in the homogenization process, nano-grade Al is generated3Er is uniformly dispersed in the crystal boundary and crystal grains in large quantity, and plays a role in refining crystal grains of the alloy in various states (as-cast state, deformation state and heat treatment state). The invention adds trace Zr and uses Al in the homogenization process3Er as the center and forming Al with a core-shell structure3The (Zr, Er) phase is uniformly and dispersedly distributed in the crystal boundary and the crystal, the recrystallization temperature of the alloy is obviously improved, the dislocation and the crystal boundary are effectively pinned, the deformation structure can be preserved and the nucleation and growth of the recrystallized grains can be inhibited in the processes of forging, solid solution and aging, the alloy has fine grain size, and the fatigue strength and the fatigue life of the alloy are improved. The precipitation and distribution of the particles are realized by matching with the optimized three-stage homogenization process, so that the aim of resisting fatigue is fulfilled. Meanwhile, the invention controls the content ratio of Mg/Si within the range of 0.5-1.2 and controls the excess Si quantity X within the range of 0.7-1.3 wt% in the Mg range by optimizing the content ratio of each component of the alloy2The strength of the alloy is improved under the combined action of Si and X; Mn/X is more than 0.1 and less than 0.8, Cr/X is more than 0.1 and less than 0.5, and micron-grade alpha-Al is generated in the casting process of Mn, Cr and Fe components15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3After the Si phase, sufficient amounts of Mn and Cr components and too muchThe residual Si generates 100nm-500nm short rod-shaped or cubic AlMnCrSi phase in the subsequent homogenization process, the AlMnCrSi phase is dispersedly distributed in the crystal grains, the size and the distribution of the AlMnCrSi phase are changed to 20nm-500nm along with the breaking of the crystal grains in the subsequent forging process, except a small part of the AlMnCrSi phase which is uniformly distributed inside and outside the crystal grains, and a large part of the AlMnCrSi phase is distributed at the grain boundary, thereby playing the roles of pinning the grain boundary and inhibiting the growth of the crystal grains on the forging structure, improving the elongation of the alloy on the premise of ensuring the strength of the alloy while improving the sub-crystal percentage of the forging structure.
The technical scheme provided by the invention separates out 5nm-10nm needle-shaped beta' -Mg at the temperature of 160-190 ℃ by an optimized semicontinuous casting process, a three-stage homogenization process, a forging process and a solid solution system and matching with a peak aging treatment process5Si6Phase-and lath-shaped Q-Al3Cu2Mg9Si7The peak aging process of 5h-8h controls the amount of precipitated phases to obtain the highest strength of the alloy; meanwhile, the high-temperature recrystallization inhibiting nanophase AlMnCrSi precipitated in the homogenization process is kept in the aging process, but the size and the shape are changed along with the change, and the nanophase AlMnCrSi is changed into particles with the particle size of 20nm-100nm, which are dispersed in the grain interior and in the grain boundary and have smooth shapes, when fatigue cracks are expanded, the particles prevent the expansion of the cracks, reduce the expansion rate of the cracks, play a role in inhibiting the expansion of the fatigue cracks, and further improve the fatigue life and the fatigue strength of the material.
The technical scheme provided by the invention optimizes alloy components, a homogenization process and a peak aging process, so that the Al-Mg-Si-Cu aluminum alloy for forging has the tensile strength of 420-440MPa and the fatigue strength of 135MPa (N is 1 multiplied by 10)7) And an excellent value of elongation of not less than 12%.
The high-strength anti-fatigue aluminum alloy material provided by the invention is suitable for producing forged parts in the fields of traffic, aviation and the like, for example, a 22.5-inch commercial vehicle high-strength ultra-light forged hub, and has the advantages of reducing weight by 2.5kg compared with a domestic hub with the same specification and reducing weight by 1kg compared with a U.S. hub, prolonging the service time by 1 year and reducing the production cost by 7%.
Drawings
FIG. 1 is a drawing of the present inventionOpen aluminum alloy cast rod homogenized transmission result Al3(Zr, Er) particle morphology graph;
FIG. 2 is a morphology chart of AlMnCrSi particles of the homogenized transmission result of the aluminum alloy cast rod disclosed by the invention;
FIG. 3 shows EBSD results of the aluminum alloy cast bars of the present disclosure in a as-forged condition;
FIG. 4 shows EBSD results of the aluminum alloy cast bar in an aged state.
Detailed Description
The present invention will be described in detail below with reference to the accompanying drawings and specific embodiments. The embodiments shown below do not limit the inventive content described in the claims. The entire contents of the configurations shown in the following embodiments are not limited to those required as solutions of the inventions described in the claims.
An aluminum alloy for casting is an Al-Mg-Si-Cu alloy, and comprises the following components in percentage by mass: 0.7-1.0 wt% of Mg, 1.0-1.7 wt% of Si, 0.35-0.5 wt% of Cu, 0.55-0.8 wt% of Mn, 0.2-0.32 wt% of Cr, 0.05-0.1 wt% of Zr, 0.05-0.15 wt% of Er, 0.02-0.05 wt% of Ti, less than or equal to 0.25 wt% of Fe, less than or equal to 0.15 wt% of the total of unavoidable impurities, and the balance of Al.
The main alloying component Mg and Si forming phase in the Al-Mg-Si-Cu series alloy is Mg2Si, the Si content in the alloy components is excessive relative to Mg, wherein the excessive Si content X plays a role in strengthening, and the content of the Mg component determines Mg2The Si content, the Si component content determines the excess Si amount X, and the Mg/Si ratio is controlled to control the Mg2Si and excess Si content. According to the technical scheme provided by the invention, the amounts of Mg and Si components are respectively controlled within the ranges of 0.75-0.95 wt% and 0.6-0.9 wt%, the Mg/Si ratio is controlled within the range of 0.5-1.2, the excess Si amount X is controlled within the range of 0.7-1.3 wt%, and a proper amount of Mg2Si and a large excess Si content X can significantly improve the alloy strength.
The invention adds the trace component Er which can generate the peritectic reaction in the casting process and can play a role in refining the crystal grains of the as-cast structure. In the homogenization process, the trace component Er forms Al with Al at the temperature of 300-350 DEG C3Er ofAl3A large amount of Er is uniformly dispersed and distributed in the crystal boundary and the crystal interior and is used as nucleation particles for subsequent dispersed phase precipitation. The invention adds trace component Zr and Al3Er is used as the center, Al3(Zr, Er) phase with a core-shell structure is formed, and is uniformly and dispersedly distributed in crystal boundaries and crystal grains, so that the recrystallization temperature of the alloy is obviously improved, dislocation and the crystal boundaries are effectively pinned, the deformation structure can be preserved and the nucleation and growth of recrystallized grains can be inhibited in the processes of forging, solution aging, the alloy has fine grain size, and the fatigue strength and the fatigue life of the alloy are improved. Matching with the optimized three-level homogenization process: keeping the temperature at 350 ℃, 400 ℃, 450 ℃ and 530 ℃, 570 ℃ for 8-12h, 6-10h and 5-11h respectively, and then performing air cooling or air cooling to realize the precipitation and distribution of the particles and achieve the purpose of resisting fatigue.
In the aluminum alloy provided by the invention, Mn/X (mass ratio) is more than 0.1 and less than 0.8, Cr/X (mass ratio) is more than 0.1 and less than 0.5, and micron-level alpha-Al can be generated by Mn, Cr components and Fe in the casting process15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3After the Si phase, enough Mn and Cr components and excessive Si content X are generated into 100nm-500nm short rod-shaped or cubic AlMnCrSi phases which are dispersedly distributed in the crystal grains in the subsequent homogenization process, the size and the distribution of the AlMnCrSi phases are changed along with the crushing of the crystal grains to 20nm-500nm granularity in the subsequent forging process, and the AlMnCrSi phases are distributed in the crystal grain boundary positions in a large amount except the crystal grains which are uniformly distributed in and out, play a role in pinning the crystal boundary to the structure, inhibiting the crystal grains from growing, improving the sub-crystal percentage of the forging structure, and improving the elongation of the alloy on the premise of ensuring the strength of the alloy.
In addition, the technical scheme provided by the invention improves the elongation of the aluminum alloy by optimizing the peak aging process, under the high-temperature peak aging process, the alloy precipitated phases are a needle-shaped beta' phase and a lath-shaped Q phase, the alloy strength is highest, and the elongation can meet the requirement of preparing the wheel hub to obtain the aluminum alloy for the wheel hub.
On the basis of reasonably adjusting the distribution ratio of each component of the aluminum alloy, the invention optimizes the semicontinuous casting process, the homogenization process, the forging process and the solid solution system and combines with low temperature and short agingA treatment process, a peak aging treatment process, and 5nm-10nm needle-shaped beta' -Mg is precipitated at the temperature of 160-190 DEG C5Si6Phase-and lath-shaped Q-Al3Cu2Mg9Si7The peak aging time of 5h-8h controls the quantity of precipitated phases, and the alloy strength is further improved; meanwhile, the high-temperature recrystallization inhibiting nano phase AlMnCrSi phase precipitated in the homogenization process is kept in the aging state process, but the size and the shape are changed along with the change, smooth particles with the appearance changed into 20nm-100nm granularity are dispersedly distributed in the crystal grain interior and the crystal boundary, and when fatigue cracks are expanded, the smooth particles can undoubtedly prevent the crack expansion and become resistance for the further expansion of the cracks, so that the fatigue life of the material is prolonged.
The technical scheme provided by the invention optimizes alloy components, three-stage homogenization process and peak aging process, so that the Al-Mg-Si-Cu aluminum alloy for forging has the tensile strength of 420-440MPa and the fatigue strength of 135MPa (N is 1 multiplied by 10)7) And an excellent value of elongation of not less than 12%. Compared with the traditional 6061 forged aluminum alloy, the tensile strength is improved by 30 percent, and the fatigue strength is improved by 13.5 percent. The alloy of the invention has various performances obviously superior to those of high-strength and high-toughness ZR6001 aluminum alloy.
The high-strength anti-fatigue aluminum alloy material provided by the invention is suitable for producing forged parts in the fields of traffic, aviation and the like, for example, a 22.5-inch commercial vehicle high-strength ultra-light forged hub, and has the advantages of reducing weight by 2.5kg compared with a domestic hub with the same specification and reducing weight by 1kg compared with a U.S. hub, prolonging the service time by 1 year and reducing the production cost by 7%.
The invention provides a preparation method of an aluminum alloy for casting, which comprises the following steps:
step 1: preparing an alloy ingot by a semi-continuous casting mode:
the semi-continuous casting comprises the steps of casting an aluminum alloy ingot with the diameter of phi 150 mm-350 mm by using water, wherein the casting speed is 40mm/min-130mm/min, the casting temperature is 680-710 ℃, and the cooling water flow is 2m3/h～20m3/h。
The pouring temperature provided by the invention prevents the phenomenon of melt overheating caused by overhigh pouring temperature, so that the ingot casting crystal grains are coarse and the mechanical property of the product is reduced; on the other hand, the phenomenon that large blocks of Cr-containing compounds are separated out due to too low pouring temperature is avoided, so that the mechanical property of subsequent forged products is sharply reduced, and even the products are scrapped.
The alloy comprises, by mass, 0.7-1.0 wt.% of Mg, 1.0-1.7 wt.% of Si, 0.35-0.5 wt.% of Cu0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.05-0.1 wt.% of Zr, 0.05-0.15 wt.% of Er0.02-0.05 wt.% of Ti, and less than or equal to 0.25 wt.% of Fe, the total amount of inevitable impurities is less than or equal to 0.15 wt.%, and the balance of Al. The Mg/Si content of the as-cast alloy is controlled to be 0.5-1.2, the excessive Si content X is 0.7-1.3 wt.%, and Mg is formed in the as-cast state2After the Si phase, the remaining amount of silicon X forms micron-sized alpha-Al 1 with Mn and Cr components5(FeMnCr)3Si2And alpha-Al12(FeMnCr)3A Si phase; Mn/X is more than 0.1 and less than 0.8, Cr/X is more than 0.1 and less than 0.5, so that enough Mn and Cr components and excessive Si components are generated in the homogenization process, and a nanoscale short rod-shaped or cubic AlMnCrSi phase is dispersed and distributed in the crystal grains. The micro component Er generates peritectic reaction in the casting process and plays a role in refining as-cast structure grains.
According to the aluminum alloy cast rod prepared by the invention, through analysis of a scanning electron microscope, the second phase of the alloy as-cast structure comprises: black rod or needle shaped Mg2Si phase, fishbone or dendritic alpha-Al (FeMn, Cr) Si phase and bright white oval Al2A Cu phase.
Step 2: homogenization treatment of alloy ingot
The high-strength anti-fatigue forged aluminum alloy is subjected to three-level homogenization process, which comprises the steps of heating an ingot in a hot air circulation annealing furnace along with the furnace to the temperature of 350-fold-sand-heat-preserving temperature of 300 ℃, 450-fold-sand-heat-preserving temperature of 400 ℃ and 570-fold-sand-heat-preserving temperature of 530 ℃ and preserving heat for 8-12h, 6-10h and 5-11h respectively.
The micro component Er forms Al with Al at the temperature of 300-3Er is uniformly dispersed in the crystal boundary and the crystal to be used as nucleation particles for the subsequent dispersed phase precipitation. The trace component Zr forms Al with Al at the temperature of 400-450 DEG C3Zr to nucleate particle Al3Er is used as the center, Al3(Zr, Er) disperse phase with nano-scale multilayer core-shell structure is precipitated and distributed between grain boundary andin the crystal, the recrystallization temperature of the alloy is obviously improved, dislocation and crystal boundary are effectively pinned, the effects of preserving deformation structure, inhibiting recrystallization and hindering the growth of crystal grains can be achieved in the processes of forging and solution aging, so that the alloy has fine crystal grain size, the fatigue strength and the fatigue life of the alloy are improved, and the aim of resisting fatigue is achieved. The trace components Cr and Mn are separated out at the temperature of 530-570 ℃ to form an AlMnCrSi phase which is in uniform and fine dispersion distribution, thereby achieving the effects of stabilizing the subgrain structure and inhibiting recrystallization.
Compared with the cast metallographic structure, the homogenized metallographic structure of the aluminum alloy rod provided by the invention has the advantages that after homogenization, a eutectic phase with a low melting point is fully dissolved, a phase containing Fe is interrupted, a phase containing Cu is completely disappeared, and Mg2Si is dispersed and finely precipitated in the crystal grains, so that dendrite segregation is eliminated, and the homogenization process is reasonable.
The homogenized transmission results of the aluminum alloy cast rod provided by the invention are shown in figures 1 and 2, and after the cast rod is homogenized in three levels, Er and Zr components generate 100-500 nm of Al with a core-shell structure3The (Zr, Er) phase is uniformly and dispersedly distributed in the crystal boundary and the crystal, the recrystallization temperature of the alloy is obviously improved, the dislocation and the crystal boundary are effectively pinned, the deformation structure can be preserved and the nucleation and growth of the recrystallized grains can be inhibited in the processes of forging and solid solution aging, and the purposes of ensuring the elongation and improving the strength and the fatigue performance of the alloy are achieved. Meanwhile, the Mn component, the Cr component and the Si component generate a short rod-shaped or cubic AlMnCrSi phase with the thickness of 100nm-500nm, and the AlMnCrSi phase is dispersed and separated out, so that the recrystallization of a subsequent forged structure is inhibited, and the subgrain percentage of the forged structure is improved.
And step 3: and (3) cooling the aluminum alloy obtained in the step (2) by air or air.
And 4, step 4: alloy ingot forging
Heating the alloy cast rod after heat treatment to 460-510 ℃ and preserving heat for 3h, forging on a hydraulic forging machine, controlling the finish forging temperature to 400-450 ℃, the forging speed to 6-20 mm/s, and the deformation not less than 0.5.
The forged EBSD result of the aluminum alloy cast rod provided by the invention is shown in FIG. 3, and the subgrain percentage in the structure is about 61%. When the percentage of the subgrain is more than or equal to 55 percent, the elongation and the fatigue strength of the material are not reduced while the strength of the material is ensured.
Al in the aluminum alloy cast rod provided by the invention3The (Zr, Er) phase is broken in the forging process, the size of the (Zr, Er) phase is 20nm-500nm, the (Zr, Er) phase is dispersed and distributed in the grain and the grain boundary, the effects of pinning dislocation and the grain boundary and inhibiting the nucleation and growth of recrystallized grains are achieved, and the aim of improving the fatigue performance is finally achieved. Meanwhile, the AlMnCrSi phase is broken, the size of the AlMnCrSi phase is 20nm-500nm, the distribution is changed along with the break, except a small part of the AlMnCrSi phase which is uniformly distributed inside and outside the crystal grains, and a large part of the AlMnCrSi phase which is distributed at the crystal grain boundary plays the roles of pinning the crystal grain boundary and inhibiting the crystal grains from growing, the subgrain percentage of the forging structure is improved, and the elongation of the alloy is finally improved.
And 5: heat treatment of forgings
a. Solution treatment: heating the high-elongation aluminum alloy forging blank obtained in the step 4 to 520-570 ℃, preserving heat for 2-3h, and then quenching with 35 ℃ water, wherein the quenching transfer time is not more than 20 s;
b. and (3) peak aging treatment: and (3) preserving the heat of the quenched sample for 5-8h at 160-190 ℃ to finish peak aging treatment.
The aging state transmission result of the aluminum alloy cast rod provided by the invention shows that the high-temperature recrystallization inhibiting nano phase AlMnCrSi precipitated in the homogenization process is remained in the aging state process, but the size and the shape are changed, the appearance is changed into smooth grains, the size is between 20nm and 100nm, the grains are dispersed and distributed in the grain interior and the grain boundary, when fatigue cracks are expanded, the grains can prevent the expansion of the cracks, the resistance of the crack expansion is increased, the effect of inhibiting the fatigue crack expansion is achieved, and therefore, the fatigue life of the material is prolonged.
The aging EBSD result of the aluminum alloy cast rod provided by the invention is shown in figure 4, the subgrain percentage in the structure is about 58%, and the subgrain percentage is slightly different from that in the forging state.
The aging state high-resolution transmission result of the aluminum alloy cast rod provided by the invention shows that 5nm-10nm needle-shaped beta' -Mg is precipitated at the aging temperature of 160-190 DEG C2Al6Si3Phase, peak aging of 5h-8h controls the amount of precipitated phase, andthe gold elongation is further improved.
Example 1
An aluminum alloy for forging comprises the following components in percentage by mass: mg: 0.7%, Si: 1.0%, Cu: 0.35%, Mn: 0.55%, Cr: 0.2%, Zr: 0.05%, Er: 0.05%, Ti: 0.02 percent, less than or equal to 0.25 percent of Fe, less than or equal to 0.15 percent of the total amount of inevitable impurities and the balance of Al. The alloy Mg/Si mass ratio is 0.5-1.2, the excess Si amount X is 0.7-1.3 wt%, the Mn/X mass ratio is 0.1-0.8, the Cr/X mass ratio is 0.1-0.5, the excess Si amount X is the amount of Mg formed2The content of Si remaining after the Si phase. The excess Si comprises micron-sized alpha-Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3Si phase, nano AlMnCrSi phase dispersed and precipitated in the homogenization process, and Si solid-dissolved in the matrix.
Example 2
An aluminum alloy for forging comprises the following components in percentage by mass: mg: 1.0 percent; si: 1.7%, Cu: 0.5%, Mn: 0.8%, Cr: 0.32%, Zr: 0.1%, Er: 0.15%, Ti: 0.05%, Fe: 0.25 percent, less than or equal to 0.15 percent of the total amount of inevitable impurities and the balance of Al. The alloy Mg/Si mass ratio is 0.5-1.2, the excess Si amount X is 0.7-1.3 wt%, the Mn/X mass ratio is 0.1-0.8, the Cr/X mass ratio is 0.1-0.5, the excess Si amount X is the amount of Mg formed2The content of Si remaining after the Si phase. The excess Si comprises micron-sized alpha-Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3Si phase, nano AlMnCrSi phase dispersed and precipitated in the homogenization process, and Si solid-dissolved in the matrix.
Example 3
An aluminum alloy for forging comprises the following components in percentage by mass: mg: 0.8%, Si: 1.2%, Cu: 0.4%, Mn: 0.7%, Cr: 0.28%, Zr: 0.07%, Er: 0.1%, Ti: 0.03%, Fe: 0.2 percent, less than or equal to 0.10 percent of the total amount of inevitable impurities and the balance of Al. The alloy Mg/Si mass ratio is 0.5-1.2, the excess Si amount X is 0.7-1.3 wt%, the Mn/X mass ratio is 0.1-0.8, the Cr/X mass ratio is 0.1-0.5, the excess Si amount X is the amount of Mg formed2Phase of SiThe Si content remaining thereafter. The excess Si comprises micron-sized alpha-Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3Si phase, nano AlMnCrSi phase dispersed and precipitated in the homogenization process, and Si solid-dissolved in the matrix.
In other embodiments of the present invention, the Mg/Si mass ratio in the aluminum alloy may be other values between 0.5 and 1.2, such as 0.6, 0.7, 0.8, 0.9, 1.0, 1.1, and the like. The excess Si amount X may be other values in the range of 0.7 to 1.3 wt%, such as 0.75 wt%, 0.8 wt%, 0.9 wt%, 1.0 wt%, 1.1 wt%, 1.2 wt%, etc. The mass ratio Mn/X may be other values between 0.1 and 0.8, for example 0.2, 0.3, 0.5, 0.7, etc. The mass ratio Cr/X may also be other values between 0.1 and 0.5, for example 0.2, 0.3, 0.4, etc.
Example 4
A preparation method of an aluminum alloy for forging comprises the following steps:
(1) preparing an aluminum alloy ingot: preparing an aluminum alloy ingot by adopting a semi-continuous casting method: casting speed is 40mm/min-130mm/min, casting temperature is 680 ℃, and cooling water flow is 2m3H, the diameter of the alloy ingot is phi 150 mm; the aluminum alloy cast ingot comprises the following components in percentage by mass: mg: 0.7%, Si: 1.0%, Cu: 0.35%, Mn: 0.55%, Cr: 0.2%, Zr: 0.05%, Er: 0.05%, Ti: 0.02 percent, less than or equal to 0.25 percent of Fe, less than or equal to 0.15 percent of the total amount of inevitable impurities and the balance of Al;
(2) three-stage homogenization treatment: sequentially preserving the aluminum alloy ingot obtained in the step (1) at 300 ℃, 400 ℃ and 530 ℃ for 8h, 6h and 5h respectively;
(3) and (3) cooling: air cooling or air cooling the aluminum alloy ingot after the three-stage homogenization treatment;
(4) forging: preserving the heat of the homogenized aluminum alloy cast ingot for 3 hours at 450 ℃, and then performing finish forging at 400 ℃, wherein the forging speed is 6mm/s, and the strain is not lower than 0.5;
(5) solid solution: carrying out solution treatment on the forged aluminum alloy material at 520 ℃ for 2 h;
(6) quenching: quenching the aluminum alloy material after solid solution;
(7) and (3) peak aging treatment: keeping the temperature of the quenched aluminum alloy material at 160 ℃ for 5 hours;
(8) and (4) processing the aluminum alloy material obtained after the peak aging treatment into an aluminum alloy product.
Example 5
A preparation method of an aluminum alloy for forging comprises the following steps:
(1) preparing an aluminum alloy ingot: preparing an aluminum alloy ingot by adopting a semi-continuous casting method: the casting speed is 130mm/min, the casting temperature is 710 ℃, and the cooling water flow is 20m3H, the diameter of the alloy ingot is phi 350 mm; the aluminum alloy cast ingot comprises the following components in percentage by mass: mg: 1.0%, Si: 1.7%, Cu: 0.5%, Mn: 0.8%, Cr: 0.32%, Zr: 0.1%, Er: 0.15%, Ti: 0.05%, Fe: 0.25 percent, less than or equal to 0.15 percent of the total amount of inevitable impurities and the balance of Al;
(2) three-stage homogenization treatment: sequentially preserving the aluminum alloy ingots obtained in the step (1) at 350 ℃, 400-;
(3) and (3) cooling: cooling the aluminum alloy cast ingot subjected to the three-stage homogenization treatment by air;
(4) forging: preserving the heat of the homogenized aluminum alloy ingot for 3 hours at 510 ℃, and then performing finish forging at 450 ℃, wherein the forging speed is 20mm/s, and the strain is 0.6;
(5) solid solution: carrying out solution treatment on the forged aluminum alloy material at 570 ℃ for 3 h;
(6) quenching: quenching the aluminum alloy material after solid solution;
(7) and (3) peak aging treatment: keeping the temperature of the quenched aluminum alloy material at 190 ℃ for 8 h;
(8) and (4) processing the aluminum alloy material obtained after the peak aging treatment into an aluminum alloy product.
Example 6
A preparation method of an aluminum alloy for forging comprises the following steps:
(1) preparing an aluminum alloy ingot: preparing an aluminum alloy ingot by adopting a semi-continuous casting method: the casting speed is 60mm/min, the casting temperature is 700 ℃, and the cooling water flow is 8m3H, the diameter of the alloy ingot is 200mm(ii) a The aluminum alloy cast ingot comprises the following components in percentage by mass: mg: 0.8%, Si: 1.2%, Cu: 0.4%, Mn: 0.7%, Cr: 0.28%, Zr: 0.07%, Er: 0.1%, Ti: 0.03%, Fe: 0.2 percent, less than or equal to 0.10 percent of the total amount of inevitable impurities and the balance of Al;
(2) three-stage homogenization treatment: respectively preserving the heat of the aluminum alloy ingot obtained in the step (1) at 315 ℃, 410 ℃ and 540 ℃ for 9h, 7h and 7 h;
(3) and (3) cooling: air cooling the aluminum alloy ingot after the three-stage homogenization treatment;
(4) forging: preserving the heat of the homogenized aluminum alloy cast ingot for 3 hours at 470 ℃, and then performing finish forging at 420 ℃, wherein the forging speed is 9mm/s, and the strain is 0.7;
(5) solid solution: carrying out solution treatment on the forged aluminum alloy material at 535 ℃ for 2.5 h;
(6) quenching: quenching the aluminum alloy material after solid solution;
(7) and (3) peak aging treatment: keeping the temperature of the quenched aluminum alloy material at 175 ℃ for 6 h;
(8) and (4) processing the aluminum alloy material obtained after the peak aging treatment into an aluminum alloy product.
The invention is further described below with reference to comparative examples:
table 1 shows the chemical compositions of the alloy disclosed by the invention and the comparative alloy in percentage by mass, wherein (i) and (ii) are the alloys in the composition range related to the invention, and (iii), (iv) and (v) are the alloys of the comparative examples. The alloy compositions shown in Table 1 were cast into round ingots with a diameter of 178mm by semi-continuous casting, and homogenized in a hot air circulation annealing furnace, and the casting process parameters and heat treatment process parameters are shown in Table 2. The ingot is homogenized and cut into cylindrical forging stock with the diameter of 150mm multiplied by 250mm by a lathe, and then the forging stock is heated to 500 ℃ and compressed along the axial direction on a hydraulic forging machine, wherein the forging process parameters are detailed in a table 3.
The forging was heat treated with the solution and aging process parameters shown in table 4, where (a) and (d) are the solution + overaging process for the alloy of the present invention, (b) (e) is the solution + peak aging process for the alloy of the present invention, (c) (f) is the solution + underaging process for the alloy of the present invention, and (e) (f) (g) is the solution + peak aging process for the alloy of the comparative example.
The structural characteristics and mechanical properties of the different alloy compositions and ageing process without the changes of the semicontinuous casting process, homogenization process and forging process are given in table 5.
TABLE 1 chemical composition of the alloys disclosed herein and comparative alloys
TABLE 2 semi-continuous casting Process parameters and homogenization Process parameters
TABLE 3 forging Process parameters
| Temperature of heating | Time of heat preservation | Open forging temperature | Temperature of the mold | Speed of forging | Amount of deformation |
| 500-510℃ | 4h | 480-500 |
200℃ | 12mm/s-15mm/s | 80％ |
TABLE 4 solid solution aging Process protocol
TABLE 5 organizational characteristics and mechanical Properties
The data in tables 1-5 illustrate that the alloy provided by the invention is prepared into round ingots with the diameter of phi 178mm by a semi-continuous casting method, and the technological parameters during stable casting are as follows: the casting speed is 120mm/min, the casting temperature is 690-700 ℃, and the cooling water flow is 2m3About/h; then, the round ingot is respectively subjected to heat preservation for 8-12h, 6-10h and 5-11h at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃ and 570 ℃ and then is subjected to air cooling to complete homogenization treatment; cutting the lathe carriage into cylindrical forging blanks with the diameter of 150mm multiplied by 250mm, heating the blanks to 500 ℃, preserving heat for 4 hours, and axially compressing the blanks on a hydraulic forging machine, wherein specific forging parameters are detailed in a table 3; the forged sample is subjected to a solid solution and peak aging heat treatment process (b), namely, the solid solution treatment is carried out for 3h at 555 ℃ and the aging treatment is carried out for 6.5h at 180 ℃, the subgrain percentage reaches 59.7%, the fatigue strength is 139MPa, the tensile strength is 437MPa, the yield strength is 385MPa, and the elongation is 13.1%.
The data in tables 1-5 illustrate that the alloys provided by the present invention (I) are processed through halfThe round ingot with the diameter of phi 178mm is prepared by the continuous casting method, and the technological parameters during stable casting are as follows: the casting speed is 120mm/min, the casting temperature is 690-700 ℃, and the cooling water flow is 2m3About/h; then, the round ingot is respectively subjected to heat preservation for 8-12h, 6-10h and 5-11h at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃ and 570 ℃ and then is subjected to air cooling to complete homogenization treatment; cutting the lathe carriage into cylindrical forging blanks with the diameter of 150mm multiplied by 250mm, heating the blanks to 500 ℃, preserving heat for 4 hours, and axially compressing the blanks on a hydraulic forging machine, wherein specific forging parameters are detailed in a table 3; the forged sample is subjected to a solid solution and peak aging heat treatment process (e), namely, the solid solution treatment is carried out at 555 ℃ for 3h and the aging treatment is carried out at 160 ℃ for 5.5h, the percentage of subgrain reaches 63.1%, the fatigue strength is 135MPa, the tensile strength is as high as 421MPa, the yield strength is 381MPa, and the elongation is 14.2%.
The alloy II provided by the invention is prepared into a round ingot with the diameter of phi 178mm by a semi-continuous casting method, and the technological parameters during stable casting are as follows: the casting speed is 120mm/min, the casting temperature is 690-700 ℃, and the cooling water flow is 2m3About/h; then, the round ingot is respectively subjected to heat preservation for 8-12h, 6-10h and 5-11h at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃ and 570 ℃ and then is subjected to air cooling to complete homogenization treatment; cutting the lathe carriage into cylindrical forging blanks with the diameter of 150mm multiplied by 250mm, heating the blanks to 500 ℃, preserving heat for 4 hours, and axially compressing the blanks on a hydraulic forging machine, wherein specific forging parameters are detailed in a table 3; the forged sample is subjected to a solid solution and low-temperature short aging heat treatment process (b), which shows that the alloy provided by the invention is subjected to solid solution treatment at 555 ℃ for 3h and aging treatment at 180 ℃ for 6.5h, the percentage of subgrain reaches 58.9%, the fatigue strength is 142MPa, the tensile strength reaches 442MPa, the yield strength is 390MPa, and the elongation is 12.6%.
The alloy II provided by the invention is prepared into a round ingot with the diameter of phi 178mm by a semi-continuous casting method, and the technological parameters during stable casting are as follows: the casting speed is 120mm/min, the casting temperature is 690-700 ℃, and the cooling water flow is 2m3About/h; then, the round ingot is respectively subjected to heat preservation for 8-12h, 6-10h and 5-11h at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃ and 570 ℃ and then is subjected to air cooling to complete homogenization treatment; cutting the lathe carriage into cylindrical forging with the diameter of 150mm multiplied by 250mmHeating the blank to 500 ℃, preserving heat for 4 hours, and compressing the blank on a hydraulic forging machine along the axial direction, wherein specific forging parameters are detailed in a table 3; the forged sample is subjected to a solid solution and low-temperature short aging heat treatment process (e), which shows that the alloy provided by the invention is subjected to solid solution treatment at 555 ℃ for 3h and aging treatment at 160 ℃ for 5.5h, the percentage of subgrain reaches 59.9%, the fatigue strength is 138MPa, the tensile strength is as high as 433MPa, the yield strength is 393MPa, and the elongation is 12.9%.
The alloy obtained by casting, three-stage homogenization, forging and (b) and (e) two kinds of solid solution and peak aging treatment has the following technical scheme that the percentage of subgrain reaches 58-63%, the fatigue strength is 135-142 MPa, the tensile strength reaches 420-437 MPa, the yield strength reaches 380-393 MPa, and the elongation rate reaches 12.6-14.4%. The tensile strength and yield strength of the alloy provided by the invention far exceed those of comparative examples, namely 6061 alloy, 6082 alloy and ZR6001 alloy, the fatigue performance is higher than that of comparative examples, namely 6061 alloy, 6082 alloy and ZR6001 alloy, and the elongation is equivalent to that of comparative examples, namely 6061 alloy, 6082 alloy and ZR6001 alloy.
In conclusion, the aluminum alloy obtained by the technical scheme provided by the invention has the comprehensive properties of strength, fatigue, elongation and the like which are far higher than those of the conventional 6061 and 6082 alloys.
The performance of a 22.5 multiplied by 9.0 inch truck forged hub made of the high-strength anti-fatigue alloy provided by the invention is evaluated by a Zhongshui automobile inspection center (Tianjin) Co., Ltd, wherein the detection of the automobile hub by a root saw GB 36581-2018 'requirements and test methods for the performance of commercial vehicle wheels' comprises two detection items of a dynamic bending fatigue test and a dynamic radial fatigue test, and the result shows that the hub produced by the high-strength anti-fatigue alloy provided by the invention by adopting a one-step forming forging process passes the performance evaluation test and meets the use requirements. The specific implementation process and performance evaluation results are as follows:
the phi 254mm high-strength anti-fatigue alloy round bar prepared by the semi-continuous casting method provided by the invention has the alloy components shown in the table 6 in detail, and the semi-continuous casting process comprises the following steps: the casting speed is 40mm/min-55mm/min, the casting temperature is 690 ℃ -700 ℃, and the cooling water flow is 15m3/h-27m3And/h, homogenizing in a hot air circulation annealing furnace, and carrying out heat preservation for 8-12h, 6-10h and 5-11h at the temperature of 350 ℃ and 450 ℃ of 400 ℃ and 570 ℃ of 530 ℃ respectively, and then carrying out air cooling.
TABLE 6 high-Strength Al alloy composition (weight%)
| Composition (A) | Si | Fe | Mg | Mn | Cu | Cr | Ti | Er | Zr | Al |
| 1# | 1.26 | 0.19 | 0.78 | 0.60 | 0.42 | 0.21 | 0.02 | 0.1 | 0.078 | Bal |
| 2# | 1.35 | 0.17 | 0.81 | 0.60 | 0.43 | 0.20 | 0.02 | 0.12 | 0.082 | Bal |
The phi 254mm cast rod of the invention is detected and analyzed, no crack exists, no loose inclusion larger than phi 1mm is found, the average grain size is about 75 μm, the maximum size of a single grain is about 180 μm, and the use requirement of the cast rod is met.
After being sawed into forged blanks with the diameter of 254mm multiplied by 295mm, the high-strength anti-fatigue alloy forged blanks provided by the invention are used for trial production of 22.5 multiplied by 9.0 inch commercial vehicle wheel hubs by using a main production process (two forging and one rotation) of the forged wheel hubs, and the main technical parameters are detailed in a table 7. The forged hub blank has no defect in appearance and good forming performance.
TABLE 7 Main technical parameters of the two-forge-one-spin forging Process
| Forging process | Temperature of heating | Temperature of preforging | Amount of pre-forging deformation | Finish forging temperature | Amount of finish forging deformation |
| Two-forging one-rotating | 500-510℃ | 480-500 |
200℃ | 70℃ | 80％ |
The heat treatment process of the high-strength anti-fatigue hub blank provided by the invention is listed in Table 9, and a 22.5 multiplied by 9.0 inch commercial vehicle high-strength ultra-light hub finished product is obtained after machining.
TABLE 9 Heat treatment process for high-strength anti-fatigue alloy hub
The dynamic bending fatigue test and the dynamic radial fatigue test of the Al alloy wheel hub provided by the invention are carried out by GB/T36581-2018 'requirements and test methods for wheel performance of commercial vehicles' in a part test room of the Zhongyun automobile inspection center (Tianjin) Limited. The test result shows that: and the wheel sample is not damaged, and the hub meets the use requirement.
The results of the hub weight, service life and mechanical properties are detailed in the table 10 after the hub ultimate fatigue bench test and the body sampling mechanical property measurement of 22.5 multiplied by 9.0 inch high-strength ultralight hubs of the high-strength anti-fatigue alloy forged commercial vehicle, 22.5 multiplied by 9.0 inch hubs of the American commercial vehicle and 22.5 multiplied by 9.0 inch common 6061 forged hubs of domestic commercial vehicles provided by the invention.
TABLE 10 mechanical properties and fatigue life of wheel hub
The test chamber and the trial-manufacture embodiment show that compared with the traditional forged 6061 alloy and 6082 alloy, the tensile strength of the high-strength anti-fatigue alloy provided by the invention reaches up to 420-440MPa, the yield strength reaches 380-395 MPa, the elongation rate reaches more than or equal to 12%, the fatigue strength reaches up to 135-145MPa, the tensile strength and the yield strength are both improved by more than 20%, and the fatigue strength is improved by about 10%. The technical scheme provided by the invention has excellent tensile strength and fatigue strength, and can meet the requirements of high strength, light weight and long service life of forged products. When the high-strength anti-fatigue Al alloy provided by the invention is used for preparing a 22.5-inch hub by a two-forging one-rotation process, the weight of the high-strength anti-fatigue Al alloy is reduced by 2.5kg compared with the weight of a domestic hub with the same specification and 1kg compared with the weight of a U.S. hub, the service time is prolonged by 1 year, the cost of each hub is saved by more than 50 yuan, and the cost is reduced by about 7%.
Finally, it should be noted that: the above embodiments are only for illustrating the technical solutions of the present invention and not for limiting the same, and although the present invention is described in detail with reference to the above embodiments, those of ordinary skill in the art should understand that: modifications and equivalents may be made to the embodiments of the invention without departing from the spirit and scope of the invention, which is to be covered by the claims.
Claims (9)
1. The aluminum alloy for forging is characterized by comprising the following components in percentage by mass: mg: 0.7-1.0%, Si: 1.0-1.7%, Cu: 0.35-0.5%, Mn: 0.55-0.8%, Cr: 0.2 to 0.32%, Zr: 0.05-0.1%, Er: 0.05-0.15%, Ti: 0.02-0.05%, Fe is less than or equal to 0.25%, the total amount of inevitable impurities is less than or equal to 0.15%, and the balance is Al.
2. The aluminum alloy for forging as recited in claim 1, wherein a mass ratio of Mg/Si in said alloy is 0.5 to 1.2, an excess Si amount X is 0.7 to 1.3 wt%, a mass ratio of Mn/X is 0.1 to 0.8, a mass ratio of Cr/X is 0.1 to 0.5, and said excess Si amount X is for forming Mg2The residual Si content in the alloy after the Si phase.
3. The aluminum forging alloy as recited in claim 2, wherein the excess Si includes micron-sized α -Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3A Si phase, a nano AlMnCrSi phase dispersed and precipitated in the homogenization process, and Si solid-dissolved in the matrix.
4. The preparation method of the aluminum alloy for forging is characterized by comprising the following steps of:
(1) preparing an aluminum alloy ingot: preparing an aluminum alloy ingot by adopting a semi-continuous casting method, wherein the aluminum alloy ingot comprises the following components in percentage by mass: mg: 0.7-1.0%, Si: 1.0-1.7%, Cu: 0.35-0.5%, Mn: 0.55-0.8%, Cr: 0.2 to 0.32%, Zr: 0.05-0.1%, Er: 0.05-0.15%, Ti: 0.02-0.05%, Fe is less than or equal to 0.25%, the total amount of inevitable impurities is less than or equal to 0.15%, and the balance is Al;
(2) three-stage homogenization treatment: sequentially preserving the aluminum alloy ingots obtained in the step (1) at the temperature of 350 ℃, 400 ℃, 450 ℃ and 530 ℃, 570 ℃ for 8-12h, 6-10h and 5-11h respectively;
(3) and (3) cooling: air cooling or air cooling the aluminum alloy ingot after the three-stage homogenization treatment;
(4) forging: forging the aluminum alloy ingot obtained in the step (3);
(5) solid solution: carrying out solution treatment on the forged aluminum alloy material;
(6) quenching: quenching the aluminum alloy material after solid solution;
(7) and (3) peak aging treatment: and carrying out peak aging treatment on the quenched aluminum alloy material.
5. The preparation method of the aluminum alloy for forging according to claim 4, wherein the step (1) of preparing the aluminum alloy ingot by the semi-continuous casting method comprises the following steps: the casting speed is 40mm/min-130mm/min, the casting temperature is 680 ℃ to 710 ℃, and the cooling water flow is 2m3/h-20m3The diameter of the alloy ingot is phi 150 mm-phi 350 mm.
6. The method for preparing an aluminum alloy for forging according to claim 4, wherein the forging method in the step (4) is: preserving the heat of the homogenized aluminum alloy ingot for 3 hours at the temperature of 450-510 ℃, and then performing finish forging at the temperature of 400-450 ℃, wherein the forging speed is 6-20 mm/s, and the strain is not lower than 0.5.
7. The method for preparing an aluminum alloy for forging as recited in claim 4, wherein the solid solution method in the step (5) is: the forged aluminum alloy material is subjected to solution treatment for 2 to 3 hours at the temperature of 520 to 570 ℃.
8. The method for preparing an aluminum alloy for forging according to claim 4, wherein the step (7) of peak aging treatment comprises: and (3) preserving the heat of the quenched aluminum alloy material for 5-8h at 160-190 ℃.
9. The method for producing an aluminum alloy for forging according to claim 4, further comprising the step (8): and (4) processing the aluminum alloy material obtained after the peak aging treatment into an aluminum alloy product.
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| CN116356169A (en) * | 2022-08-08 | 2023-06-30 | 台州学院 | Preparation method of high-strength high-toughness aluminum alloy for high-speed rail |
| CN115572871A (en) * | 2022-10-31 | 2023-01-06 | 山东骏程金属科技有限公司 | Commercial aluminum alloy forged wheel and preparation method thereof |
| CN115572871B (en) * | 2022-10-31 | 2023-09-15 | 山东骏程金属科技有限公司 | Commercial aluminum alloy forged wheel and preparation method thereof |
| CN116200631A (en) * | 2023-03-09 | 2023-06-02 | 魏桥轻量化(苏州)科技有限公司 | A kind of 6xxx aluminum alloy and preparation method thereof |
| CN116334455A (en) * | 2023-03-09 | 2023-06-27 | 魏桥轻量化(苏州)科技有限公司 | Preparation method and application of aluminum alloy extruded profile |
| CN117127065A (en) * | 2023-10-23 | 2023-11-28 | 中铝材料应用研究院有限公司 | Aluminum alloy material and preparation method thereof |
| CN117127065B (en) * | 2023-10-23 | 2024-02-13 | 中铝材料应用研究院有限公司 | Aluminum alloy material and preparation method thereof |
| CN119194189A (en) * | 2024-11-26 | 2024-12-27 | 莱州新安达汽车零部件有限公司 | A preparation process of high-strength aluminum alloy |
| CN119194189B (en) * | 2024-11-26 | 2025-02-11 | 莱州新安达汽车零部件有限公司 | Preparation process of high-strength aluminum alloy |
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