CN113215447A - Al-Mg-Si-Cu alloy for hub - Google Patents
Al-Mg-Si-Cu alloy for hub Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 125
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 120
- 229910018594 Si-Cu Inorganic materials 0.000 title claims abstract description 57
- 229910008465 Si—Cu Inorganic materials 0.000 title claims abstract description 57
- 238000005242 forging Methods 0.000 claims abstract description 98
- 238000000034 method Methods 0.000 claims abstract description 60
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- 239000011159 matrix material Substances 0.000 claims description 2
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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
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23P—METAL-WORKING NOT OTHERWISE PROVIDED FOR; COMBINED OPERATIONS; UNIVERSAL MACHINE TOOLS
- B23P15/00—Making specific metal objects by operations not covered by a single other subclass or a group in this subclass
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- 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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Abstract
The invention provides an Al-Mg-Si-Cu alloy for a hub, which comprises the following components in percentage by mass: 0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of Ti, less than or equal to 0.25 wt.% of Fe, less than or equal to 0.15 wt.% of the total unavoidable impurities, and the balance of Al. The preparation method of the alloy product comprises the following steps: preparing an alloy ingot by adopting a semi-continuous casting method; homogenizing in a hot air circulation annealing furnace, keeping the temperature at 520-570 ℃, then carrying out air cooling after 5-11h or carrying out air cooling, then carrying out forging at 450-510 ℃, controlling the final forging temperature at 400-450 ℃, and controlling the strain quantity to be not less than 0.5; then, carrying out heat treatment on the forged piece, carrying out solution treatment at 520-570 ℃ for 2-3 h, then carrying out underaging treatment after quenching, and carrying out heat preservation at 150-170 ℃ for 2-3 h; and finally, machining to obtain a finished product. The obtained forging has excellent elongation percentage of 15-18%, higher yield strength of 310-330MPa and fatigue strength of 130-135MPa, is suitable for producing forging products with one-step forming and large strain capacity, such as commercial vehicle hubs, and can greatly improve the toughness, fatigue life and yield of the hubs and reduce the production cost.
Description
Technical Field
The invention relates to a non-ferrous metal material, in particular to an Al-Mg-Si-Cu alloy for a hub 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, the yield strength of the product is 280MPa, the tensile strength is 320MPa, and the elongation is 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 aging, so that the necessary premise of improving the fatigue performance and prolonging the fatigue life of the hub is that the aluminum alloy forged hub is widely applied. 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 finished product rate of the product 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.
Therefore, in order to meet the requirements of automobile safety and advanced forging technology on material performance, improve the toughness and fatigue life of the wheel hub, improve the yield of wheel hub formed by one-forging and realize further light weight, the Al-Mg-Si-Cu alloy which has the elongation rate far superior to that of 6061 aluminum alloy and has the strength superior to that of 6061 aluminum alloy is required to be provided.
Disclosure of Invention
Aiming at the defects of the prior art, the invention provides the high-elongation Al-Mg-Si-Cu alloy for the wheel hub and the preparation method thereof, and the invention is realized by the following technical scheme:
the high-elongation Al-Mg-Si-Cu alloy for forging is characterized by comprising the following components in percentage by mass: 0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of Ti, less than or equal to 0.25 wt.% of Fe, less than or equal to 0.15 wt.% of the total unavoidable impurities, and the balance of Al.
Further, the above-mentioned high elongation Al — Mg-Si-Cu alloy for forging is characterized in that: the Mg/Si content of the alloy is controlled to be 0.9-1.8, the content of surplus Si is recorded as X, X is 0.1-0.6, Mn/X is more than 1 and less than 8, Cr/X is more than 0.3 and less than 3.2, after homogenization, forging and solution treatment, a semicontinuous alloy ingot is subjected to underaging treatment at the temperature of 150-170 ℃ for 2-3 h, the yield strength of the material is 310-340 MPa, and the elongation is 15-18%.
Further, the above-mentioned excess Si content means that Mg is formed in the alloy2After Si, the remaining total Si content, the presence of excess Si for the high elongation Al-Mg-Si-Cu alloy for forgingThe form comprises the following types of alpha-Al with micron scale15(FeMnCr)3Si2、α-Al12(FeMnCr)3Si phase and nano AlMnCrSi phase, and the contents of Si and simple substance Si which are solid-dissolved in the matrix are weak.
The preparation method of the high-elongation Al-Mg-Si-Cu alloy for forging comprises the following steps of firstly, preparing an alloy ingot by adopting a semi-continuous casting mode, and controlling the component contents of Mg to be 0.75-0.95 wt.%, Si to be 0.6-0.9 wt.%, Cu to be 0.35-0.5 wt.%, Mn to be 0.55-0.8 wt.%, Cr0.2-0.32 wt.%, Ti to be 0.02-0.05 wt.%, Fe to be less than or equal to 0.25 wt.%, the total amount of inevitable impurities to be less than or equal to 0.15 wt.%, and the balance of Al in the manufacturing process; then homogenizing, heating the ingot in a hot air circulation annealing furnace to 520-570 ℃, preserving the temperature for 5-11h, and then air cooling or air cooling; then forging, heating the homogenized cast ingot to 450-510 ℃ for forging, ensuring that the finish forging temperature is not lower than 400 ℃ (the finish forging temperature is 400-450 ℃), the forging speed is 6-20 mm/s, and the strain is not lower than 0.5; and finally, carrying out heat treatment on the forged piece, carrying out solution treatment for 2-3 h at 520-570 ℃, quenching, carrying out underaging treatment, and carrying out heat preservation for 2-3 h at 150-170 ℃.
Furthermore, the preparation method of the high-elongation Al-Mg-Si-Cu alloy for forging is characterized by comprising the following steps: the semi-continuous casting mode is a direct water-cooling casting mode, the diameter of an alloy ingot prepared by the semi-continuous casting mode is phi 150 mm-350 mm, the casting speed is 40 mm/min-130 mm/min, and the pouring temperature is 680-710 ℃; the flow rate of cooling water is controlled at 2m3/h～20m3/h。
Compared with the closest prior art, the technical scheme provided by the invention has the following excellent effects: according to the invention, the content ratio of each component of the alloy is optimized, Mg/Si is controlled within the range of 0.9-1.8, and the excess Si amount X is controlled within the range of 0.1-0.6 wt.% of Mg2The strength of the alloy is improved under the combined action of Si and X; Mn/X is more than 1 and less than 8, Cr/X is more than 0.3 and less than 3.2, and micron-grade alpha-Al 1 is generated in the casting process of Mn, Cr and Fe components5(FeMnCr)3Si2And alpha-Al12(FeMnCr)3After the Si phase, a sufficient amount of Mn,The Cr component and the excessive Si generate 100nm-500nm short rod-shaped or cubic AlMnCrSi phase which is dispersed and distributed in the crystal grains in the subsequent homogenization process, the size and the distribution of the AlMnCrSi phase are changed to 20nm-500nm along with the crushing of the crystal grains in the subsequent forging process, except for small parts which are uniformly distributed inside and outside the crystal grains, most of the AlMnCrSi phase is distributed at the crystal grain boundary, and the AlMnCrSi phase plays the roles of pinning the crystal boundary and inhibiting the growth of the crystal grains on the forging structure, so that the elongation of the alloy is improved on the premise of ensuring the strength of the alloy while the sub-crystal percentage of the forging structure is improved.
The technical scheme provided by the invention separates out 5nm-10nm needle-shaped initial-beta' -Mg at the lower temperature of 150-170 ℃ through reasonable semicontinuous casting process, homogenization process, forging process and solid solution system and matching with low-temperature short aging treatment process2Al6Si3The number of precipitated phases is controlled by the short aging process of 2.5-3 h, so that the elongation of the alloy is further improved; 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 of the material.
The technical scheme provided by the invention optimizes alloy components and a low-temperature short-aging process, so that the elongation of the Al-Mg-Si-Cu aluminum alloy for forging reaches 15-18%, the yield strength reaches 310-330MPa, and the fatigue strength reaches 135MPa (N is 1 multiplied by 10)7) Such an excellent value.
The fact that the high-elongation and high-fatigue-strength aluminum alloy material provided by the invention is applied to the production of closed backward extrusion forging hub formed by one-forging shows that the toughness and fatigue life of the hub are greatly improved, the yield of the hub formed by one-forging is greatly increased, and the production cost is reduced.
Drawings
The technical scheme provided by the invention is further explained by combining the accompanying drawings as follows:
FIG. 1: the Al-Mg-Si-Cu alloy cast rod provided by the invention has an as-cast metallographic structure;
FIG. 2: DSC curve chart of Al-Mg-Si-Cu alloy cast rod provided by the invention
FIG. 3: the Al-Mg-Si-Cu alloy cast rod provided by the invention has a homogeneous metallographic structure
FIG. 4: the Al-Mg-Si-Cu alloy cast rod provided by the invention has a uniform transmission result
FIG. 5: the invention provides an EBSD result of the Al-Mg-Si-Cu alloy cast rod in a forging state
FIG. 6: the invention provides the transmission result of the Al-Mg-Si-Cu alloy cast rod in the forging state
FIG. 7: the Al-Mg-Si-Cu alloy cast rod provided by the invention has an aging state transmission result
FIG. 8: the invention provides an aging state EBSD result of the Al-Mg-Si-Cu alloy cast rod
FIG. 9: the Al-Mg-Si-Cu alloy cast rod provided by the invention has an aging state high-resolution transmission electron microscope result
FIG. 10: 22-inch commercial vehicle hub structure diagram prepared by adopting one-forging forming process by using Al-Mg-Si-Cu alloy provided by the invention
Detailed Description
An Al-Mg-Si-Cu alloy for hubs comprises the following components in percentage by mass: 0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of Ti, less than or equal to 0.25 wt.% of Fe, less than or equal to 0.15 wt.% of the total 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, wherein the excess Si amount X plays a strengthening role, and the content of the Mg component determines Mg2Si content, Si component content determining the excess Si amount X, Mg/Si control2Si 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.%, Mg/Si is controlled within the range of 0.9-1.8, X is controlled within the range of 0.1-0.6, and a proper amount of Mg is added2Si and a small excess Si content X can suitably improve the alloy strengthDegree;
wherein Mn/X is more than 1 and less than 8, Cr/X is more than 0.3 and less than 3.2, thereby ensuring that micron-grade alpha-Al is generated by Mn and 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 Al-Mg-Si-Cu alloy for the wheel hub by optimizing the short aging process, and under the high-temperature peak aging process, the alloy precipitated phases are a needle-shaped beta 'phase and a lath-shaped Q' phase, so that the alloy strength is highest, and the elongation can meet the requirement of the wheel hub.
The needle-shaped initial-beta' phase precipitated from the alloy under the low-temperature short-aging process is large in quantity and small in size, and during high-temperature peak aging, on the premise of ensuring the strength of the alloy, the toughness of the alloy is increased, and the elongation of the alloy is improved. The invention adopts a low-temperature underaging process, and the material with yield strength of 310MPa-330MPa and elongation of 15% -18% is obtained by underaging treatment at 150-170 ℃ for 2-3 h. Compared with the traditional 6061 forged aluminum alloy, the elongation is improved by 35%, the yield strength is improved by 11%, and the fatigue strength is improved by 13.5%. The elongation is obviously superior to that of the high-strength high-toughness ZR6001 aluminum alloy. In addition, the alloy provided by the invention is used for preparing the hub according to the closed backward extrusion forging hub production process formed by one-forging, and the yield of the hub is improved by more than 3%.
On the basis of reasonably adjusting the component proportion of the Al-Mg-Si-Cu alloy, the invention optimizes the semicontinuous casting process, the homogenization process, the forging process and the solid solution system, and is matched with the low-temperature short aging treatment process to precipitate 5n at the lower temperature of 150-170 DEG CNeedle-shaped initial-beta' -Mg with m-10nm2Al6Si3The amount of precipitated phases is controlled by short aging for 2-3 h, and the elongation of the alloy 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, and smooth particles with the appearance changed into 20nm-100nm granularity are dispersedly distributed in the crystal grain interior and the crystal boundary, when fatigue cracks are expanded, the smooth particles can undoubtedly prevent the crack expansion and become resistance for the further expansion of the cracks, thereby improving the fatigue life of the material. The invention optimizes the alloy components and the low-temperature short-aging process to ensure that the Al-Mg-Si-Cu aluminum alloy for forging achieves excellent elongation, higher yield strength and fatigue strength, wherein the elongation is 15-18 percent, the yield strength is 310-330MPa, and the fatigue strength is 135MPa (N is 1 multiplied by 10)7). The high-elongation high-fatigue-strength aluminum alloy material provided by the invention is used for forging the hub in a closed backward extrusion manner by one-forging, so that the toughness and the fatigue life of the hub and the yield of the one-forging hub are improved, and the production cost is reduced.
The preparation method of the high-elongation Al-Mg-Si-Cu alloy for forging provided by the invention comprises the following steps:
step 1: preparing an alloy ingot by a semi-continuous casting mode:
the semi-continuous casting comprises the steps of using Al-Mg-Si-Cu alloy cast ingot with the water cooling diameter of phi 150 mm-350 mm, wherein the casting speed is 40 mm/min-130 mm/min, the casting temperature is 680 ℃ to 710 ℃, and the cooling water flow is 2m3/h～20m3/h。
The casting temperature provided by the invention prevents the phenomenon of overburning of the melt caused by overhigh casting temperature, so that the crystal grains of the cast ingot are coarse, and the mechanical property of the product can be reduced; on the other hand, the phenomenon that large blocks of Cr-containing compounds are separated out when the casting temperature is too low 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, 0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of TiThe total content of inevitable impurities is less than or equal to 0.15 wt.%, and the balance is Al. The Mg/Si content of the as-cast alloy is controlled to be 0.9-1.8, the excess Si content X is 0.1-0.6, 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 1 and less than 8, Cr/X is more than 0.3 and less than 3.2, so that enough Mn and Cr components and excessive Si components are ensured to generate nanoscale short rod-like or cubic AlMnCrSi phases which are dispersed and distributed in the crystal grains in the subsequent homogenization process.
The high-elongation Al-Mg-Si-Cu alloy rod for forging has an as-cast metallographic structure as shown in figure 1, and through analysis of a scanning electron microscope, the as-cast second phase of the alloy comprises the following components in parts by weight: 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 homogenizing process of the high-elongation Al-Mg-Si-Cu alloy for forging comprises the steps of heating an ingot in a hot air circulation annealing furnace to 520-570 ℃, keeping the temperature for 5-11h, then cooling by air or cooling by air, and measuring a DSC (differential scanning calorimetry) measurement curve of the melting point of a low-melting-point eutectic compound in a cast rod by using a Differential Scanning Calorimetry (DSC), wherein the DSC measurement curve is as shown in figure 2, so that the melting point of the low-melting-point eutectic compound of the Al-Mg-Si-Cu alloy material is 573 ℃, which shows that dendritic crystals are improved, the low-melting-point eutectic phase is eliminated, trace components Cr and Mn are uniformly and finely dispersed and distributed, a subgrain structure is stabilized, recrystallization is inhibited, and the tissue overburning phenomenon in the homogenizing process is prevented.
The homogenized metallographic structure of the Al-Mg-Si-Cu alloy rod provided by the invention is shown in figure 3, which shows that compared with the cast metallographic structure, the homogenized metallographic structure is more intermittent, the second phase is fully dissolved, the aggregation condition is obviously improved, and the Cu-containing phase completely disappears, thus the homogenization process is reasonable.
The Al-Mg-Si-Cu alloy cast rod provided by the invention has a homogenized transmission result as shown in figure 4, and after the cast rod is homogenized according to the technical scheme provided by the invention, Mn and Cr components and Si components generate a 100-500 nm short rod-shaped or cubic AlMnCrSi phase, and the AlMnCrSi phase is dispersed and precipitated, so that the recrystallization of a subsequent forged structure is inhibited, and the subgrain percentage of the forged structure is improved.
And step 3: alloy ingot forging
Heating the alloy cast rod after heat treatment to 450-510 ℃, preserving heat for 3h, forging on a hydraulic forging machine, controlling the finish forging temperature to 400-450 ℃, the forging speed to be 6-20 mm/s, deforming once in place and the strain amount to be not less than 0.5.
The forging EBSD result of the Al-Mg-Si-Cu alloy cast rod provided by the invention is shown in figure 5, the subgrain percentage in the structure is about 76%, and the elongation can be improved while the strength of the material is ensured by improving the subgrain percentage.
The transmission result of the Al-Mg-Si-Cu alloy cast rod in the forging state is shown in figure 6, which shows that AlMnCrSi phase generated in the homogenization process is broken, the size of the AlMnCrSi phase is 20nm-500nm, the distribution of the AlMnCrSi phase is changed along with the size, except that a small part of the AlMnCrSi phase is uniformly distributed inside and outside crystal grains, and a large part of the AlMnCrSi phase is distributed at the crystal grain boundary, so that the Al-Mg-Si-Cu alloy cast rod plays roles in pinning the crystal grain boundary and inhibiting the growth of the crystal grains for the tissue, and the subgrain percentage of the forging tissue is improved.
And 4, step 4: heat treatment of forgings
4a solution treatment: heating the high-elongation Al-Mg-Si-Cu alloy forging blank obtained in the step 3 to 520-570 ℃, preserving heat for 2-3 h, and then carrying out water quenching at 35 ℃ for not more than 20 s;
4b underaging treatment: and (3) preserving the heat of the quenched sample at 150-170 ℃ for 2-3 h to finish underaging treatment.
The aging state transmission result of the Al-Mg-Si-Cu alloy cast rod provided by the invention is shown in figure 6, and the result shows that the high-temperature recrystallization inhibiting nano phase AlMnCrSi precipitated in the homogenization process is retained in the aging state process, but the size and the shape are changed, the appearance is changed into smooth grains, the size is 20nm-100nm, the grains are dispersedly 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 preventing the expansion of the fatigue cracks is achieved, and the fatigue life of the material is prolonged.
The aging EBSD result of the Al-Mg-Si-Cu alloy cast rod provided by the invention is shown in figure 7, and the subgrain percentage in the structure is about 74.6%, and the subgrain percentage is slightly different from that in the forging state.
The aging state high resolution transmission result of the Al-Mg-Si-Cu alloy cast rod provided by the invention is shown in figure 8, and the result shows that 5nm-10nm needle-shaped initial-beta' -Mg is precipitated at the aging temperature of 150 ℃ -170 DEG C2Al6Si3The amount of precipitated phases is controlled within 2-3 h, and the elongation of the alloy is further improved.
The embodiments of the present invention are further described below with reference to specific examples:
table 1 shows the chemical compositions of the alloys of examples and comparative examples in terms of mass percent, wherein (i) and (ii) are alloys within the composition range according to the present invention, and (iii), (iv) and (v) are alloys of comparative examples. The alloy compositions shown in Table 1 were cast into round ingots having a diameter of 154mm 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 is heat treated by the parameters of the solid solution and aging process shown in the table 4, wherein (a) is the solid solution and overaging process, (b) (c) (d) is the solid solution and peak aging process, and (e) (f) (g) is the solid solution and low temperature short aging process.
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 compositions of alloys of examples and comparative examples
TABLE 2 semi-continuous casting Process parameters and homogenization Process parameters
TABLE 3 forging Process parameters
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 154mm 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 subjected to heat preservation for 11 hours at the temperature of 560 ℃ 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 solid solution and low-temperature short aging heat treatment process (f), namely solid solution treatment at 530 ℃ for 3h and aging treatment at 160 ℃ for 3h, the percentage of subgrain reaches 76.8 percent, and fatigue is causedThe labor strength is 133MPa, the tensile strength is 382MPa, the yield strength is 314MPa, and the elongation rate is up to 17 percent.
The data in tables 1-5 also show that the alloy provided by the invention is prepared into round ingots with the diameter of phi 154mm 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 subjected to heat preservation for 11 hours at the temperature of 560 ℃ 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 (g), which shows that the alloy provided by the invention is subjected to solid solution treatment at 530 ℃ for 3h and aging treatment at 160 ℃ for 2.5h, the percentage of subgrain reaches 79.3%, the fatigue strength is 134MPa, the tensile strength is 391MPa, the yield strength is 320MPa, and the elongation is as high as 18%.
The alloy II provided by the invention is prepared into a round ingot with the diameter of phi 154mm 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 subjected to heat preservation for 11 hours at the temperature of 560 ℃ 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 (f), which shows that the alloy 2 provided by the invention is subjected to solid solution treatment at 530 ℃ for 3h and aging treatment at 160 ℃ for 3h, the percentage of subgrain reaches 74.6%, the fatigue strength is 132MPa, the tensile strength is 390MPa, the yield strength is 322MPa, and the elongation is as high as 16%.
The alloy II provided by the invention is prepared into a round ingot with the diameter of phi 154mm 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 subjected to heat preservation for 11 hours at the temperature of 560 ℃ 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 solid solution treatment and low-temperature short aging heat treatment process (g), which shows that after the alloy provided by the invention is subjected to solid solution treatment at 530 ℃ for 3h and aging treatment at 160 ℃ for 2.5h, the percentage of subgrain reaches 73.3%, the fatigue strength is 135MPa, the tensile strength is 387MPa, the yield strength is 310MPa, and the elongation is as high as 16.3%.
The invention provides the technical scheme that after casting, homogenizing, forging and (f) (g) two kinds of solid solution and low-temperature short aging treatment, the alloy is subjected to the first step and the second step, the percentage of subgrain reaches 73-80%, the fatigue strength is 130-135MPa, the tensile strength reaches 380-390 MPa, the yield strength reaches 310-320 MPa, and the elongation rate reaches 16-18%. The elongation of the alloy provided by the invention far exceeds that of a 6061 alloy, a fifthly 6082 alloy and a GR6001 alloy, the strength is higher than that of the 6061 alloy and the fifthly 6082 alloy, and the fatigue performance is higher than that of the 6061 alloy and the fifthly 6082 alloy.
In conclusion, the comprehensive performances of the aluminum alloy obtained by the technical scheme provided by the invention, such as elongation, strength, fatigue and the like, are far higher than those of the conventional 6061 and 6082 alloys.
The performance of a 22-inch Karba vehicle forging hub made of the Al-Mg-Si-Cu alloy provided by the invention is evaluated by Zhongyamo automobile inspection center (Tianjin) Co., Ltd, wherein the detection of the automobile hub by a saw GB/T5909-. The specific implementation process and performance evaluation results are as follows:
the alloy components of three round bars with phi 305mm of Al-Mg-Si-Cu alloy prepared by the semi-continuous casting method are detailed in a table 6, and the semi-continuous casting process comprises the following steps: the casting speed is 40mm/min-55mm/min, the casting temperature is 690 ℃ -710 ℃, and the cooling water flow is 15m3/h-27m3H in hot airHomogenizing in a circulating annealing furnace at 560 ℃ for 11 hours.
TABLE 6 high elongation Al-Mg-Si-Cu alloy composition (weight%)
| Composition (I) | Si | Fe | Cu | Mn | Mg | Cr | Ti | Al |
| 1# | 0.78 | 0.09 | 0.46 | 0.65 | 0.82 | 0.26 | 0.03 | The rest(s) |
| 2# | 0.77 | 0.10 | 0.47 | 0.63 | 0.84 | 0.26 | 0.03 | The rest(s) |
| 3# | 0.77 | 0.10 | 0.47 | 0.65 | 0.82 | 0.25 | 0.03 | The rest(s) |
The phi 305mm cast rod of the invention is detected and analyzed, has no crack, has no loose inclusion larger than phi 1mm, has the average grain size of about 150 mu m, and has the maximum size of about 270 mu m of single grain, thereby meeting the use requirement of the cast rod.
The material was sawed into 15 forged blanks of approximately 305mm phi by 250mm phi as shown in FIG. 9.
A closed backward extrusion forging process is used, the Al-Mg-Si-Cu alloy forging blank provided by the invention is used for trial production of a 22-inch truck hub by one-forging forming, and the main technical parameters are detailed in a table 7.
TABLE 7 main technical parameters of closed backward extrusion forging process
| Forging process | Temperature of heating | Open forging temperature | Temperature of the mold | Forging forming time | Amount of deformation |
| Closed backward extrusion | 500-510℃ | 480-500℃ | 200℃ | 70s | 80％ |
The data obtained after forging each billet into a hub during closed backward extrusion forging is detailed in table 8.
Table 822 inch truck forged hub data
Table 8 shows that 15 forged blanks made of the Al-Mg-Si-Cu alloy provided by the invention are completely formed, and the appearance is free of defects, so that the Al-Mg-Si-Cu alloy provided by the invention has excellent elongation, the percentage of subgrain in a forged structure is more than 70%, and the yield of wheel hubs formed by one forging is improved.
The heat treatment process of the Al-Mg-Si-Cu alloy truck forged hub provided by the invention is listed in Table 9, and the finished product structure of the 22-inch commercial truck hub after machining is shown in FIG. 10.
TABLE 9 high-elongation Al-Mg-Si-Cu alloy hub heat treatment process
Part laboratory of the middle automobile research center (Tianjin) GmbH. The dynamic bending fatigue test and the dynamic radial fatigue test of the Al-Mg-Si-Cu alloy wheel hub provided by the invention are carried out according to GB/T5909-plus 2009 'commercial vehicle wheel performance requirement and test method'.
The test result shows that: the dynamic bending fatigue test is circulated for 30 ten thousand times, and the wheel sample is not damaged; dynamic radial circulation fatigue test is carried out for 180 ten thousand times, the test shows that the wheel sample is not damaged, and the hub meets the use requirement.
The above test chamber and trial-manufacture example show that compared with the traditional forged 6061 alloy and 6082 alloy, the Al-Mg-Si-Cu alloy provided by the invention has the elongation rate of 16-18%, the tensile strength of 380-390 MPa, the yield strength of 310-320 MPa, the fatigue strength of 130-135MPa, the yield strength of 11%, the elongation of 35% and the fatigue strength of 10%. The excellent fatigue strength of the technical scheme provided by the invention can not only improve the fatigue life of the hub, but also improve the transportation safety and stability of the load-carrying commercial vehicle. Moreover, due to the excellent elongation and high strength of the technical scheme provided by the invention, the Al-Mg-Si-Cu alloy provided by the invention can also be suitable for an advanced closed backward extrusion forging process, which undoubtedly also can improve the yield of one-step forming of large-size forged parts. In addition, when the Al-Mg-Si-Cu alloy provided by the invention is used for forging a 22-inch hub by closed backward extrusion technology, the weight of the hub is reduced by 4%, the yield is improved by 3%, and the cost of each hub is saved by 135 yuan and reduced by 17%.
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 (4)
1. An Al-Mg-Si-Cu alloy for wheel hubs, characterized in that said alloy comprises, in mass percent: 0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of Ti, less than or equal to 0.25 wt.% of Fe, less than or equal to 0.15 wt.% of the total amount of unavoidable impurities, and the balance of Al;
the mass ratio of the Mg/Si alloy is 0.9-1.8, the excessive Si amount X is 0.1-0.6 wt.%, Mn/X is more than 1 and less than 8, and Cr/X is more than 0.3 and less than 3.2;
the preparation method of the alloy product comprises the following steps:
1-1, carrying out homogenization, forging and solution treatment on the alloy ingot cast by semicontinuous casting;
1-2, performing low-temperature short-time aging treatment at the temperature of 150-170 ℃ for 2-3 h;
1-3 machining into a product.
2. The Al-Mg-Si-Cu alloy for wheel hubs according to claim 1,
si, Mn and Cr components form a nanoscale AlMnCrSi phase which is dispersed and distributed in a crystal boundary and an intragranular position to block the growth of forging crystal grains, so that the subgrain percentage of a forging structure is more than or equal to 70 percent;
the excess Si being Mg2The amount of Si remaining after Si phase, said remaining amount of Si comprising micron-sized alpha-Al15(FeMnCr)3Si2And alpha-Al12(FeMnCr)3Si phase, nano AlMnCrSi phase dispersed and precipitated in the homogenization process, trace simple substance Si and Si dissolved in the matrix.
3. The Al-Mg-Si-Cu alloy for wheel hubs of claim 1, wherein said method comprises:
1-1-1, preparing an alloy ingot with the following components in percentage by mass by a semi-continuous casting method:
0.75-0.95 wt.% of Mg, 0.6-0.9 wt.% of Si, 0.35-0.5 wt.% of Cu, 0.55-0.8 wt.% of Mn, 0.2-0.32 wt.% of Cr, 0.02-0.05 wt.% of Ti, less than or equal to 0.25 wt.% of Fe, less than or equal to 0.15 wt.% of the total amount of unavoidable impurities, and the balance of Al;
1-1-2, homogenizing the obtained alloy ingot:
preserving the heat in a hot air circulating annealing furnace at the temperature of 520-570 ℃ for 5-11h, and then air cooling or air cooling;
1-1-3, wherein the forging comprises forging the homogenized cast ingot at 450-510 ℃, and finish forging at 400-450 ℃, wherein the forging speed is 6-20 mm/s, and the strain is not lower than 0.5;
1-1-4, wherein the solution treatment comprises the steps of performing solution treatment on the forge piece for 2-3 hours at the temperature of 520-570 ℃, and quenching.
4. The Al-Mg-Si-Cu alloy for wheel hubs according to claim 3, wherein:
the semi-continuous casting of step 1-1-1 includes,
casting alloy ingot with diameter of phi 150-350 mm by water cooling, wherein the casting speed is 40-130 mm/min, the casting temperature is 680-710 ℃, and the cooling water flow is 2m3/h～20m3/h。
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