CN113245486B - Preparation method of die forging of Al-Mg-Si series aluminum alloy for inhibiting coarse grain structure - Google Patents
Preparation method of die forging of Al-Mg-Si series aluminum alloy for inhibiting coarse grain structure Download PDFInfo
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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
- B21J5/02—Die forging; Trimming by making use of special dies ; Punching during forging
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21K—MAKING FORGED OR PRESSED METAL PRODUCTS, e.g. HORSE-SHOES, RIVETS, BOLTS OR WHEELS
- B21K29/00—Arrangements for heating or cooling during processing
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
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- C22C1/03—Making non-ferrous alloys by melting using master alloys
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- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
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- 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
- C22F1/04—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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Abstract
A preparation method of a die forging of Al-Mg-Si series aluminum alloy for inhibiting a coarse grain structure comprises the following components in percentage by mass: 0.4 to 1.5 percent of Mg, 0.3 to 1.5 percent of Si, 0.01 to 0.7 percent of Cu, 0.01 to 0.3 percent of Fe, 0.01 to 1.0 percent of Mn, 0.001 to 0.25 percent of Zr, 0.01 to 0.5 percent of Cr, 0.001 to 0.25 percent of Sc, 0.01 to 0.1 percent of V, 0.01 to 0.25 percent of Ti and other transition group elements, and the preparation method comprises the following steps: cleaning and purifying a melt, casting a plurality of near-forging hot tops, homogenizing at a multi-stage speed control mode, performing die forging forming at room temperature or high temperature, and performing two-stage solid solution and aging treatment. The die forging prepared has no coarse grain or coarse grain structure characteristics, has excellent fatigue resistance and anodic oxidation resistance, and can be used for preparing aluminum alloy structural members of vehicles, transportation vehicles and transportation tools.
Description
Technical Field
The invention belongs to the field of aluminum alloy processing and preparation, and particularly relates to a preparation method of a die forging of Al-Mg-Si series aluminum alloy for inhibiting a coarse grain structure.
Background
Al-Mg-Si series aluminum alloy belongs to heat treatment strengthening type aluminum alloy, and Mg precipitated after solid solution aging2The Si phase is a main strengthening phase of the alloy, so that the alloy has excellent strength, elongation and good processability, meanwhile, in order to meet the application requirements of complex fields such as rail traffic, vehicles and the like, transition elements such as Mn, Cr and the like are required to be added into the Al-Mg-Si series aluminum alloy, so that the alloy has better hardenability, impact toughness and corrosion resistance while ensuring the strength, and can replace a steel structure to realize the light weight effect of reducing weight by 30-40%. The aluminum alloy die forging technology is that the aluminum alloy blank is in a hot state by utilizing a die on special equipmentAnd then the aluminum product with excellent mechanical performance is obtained. The Al-Mg-Si series aluminum alloy die forging piece combines the characteristics of heat treatment strengthening, high size stability of die forging forming and excellent product performance of the alloy, becomes the first choice of vehicle light weight, and is processed into ultralight structural parts such as connecting rods, sleeper beams, rims, hubs, swing arms and the like.
In order to ensure the product performance, the Al-Mg-Si series aluminum alloy die forging piece generally adopts an extrusion material as a forging blank, and is subjected to 2-3 times of die forging thermal deformation to obtain a finished product for machining and surface treatment. Most of aluminum alloy die forgings applied to vehicles are safety structural parts, strict mechanical property requirements are met, the fatigue strength and the durable life of the structure are ensured, and coarse-grained structures are absolutely not allowed to appear at key positions such as bearing force or reinforcing ribs of the die forgings. However, the position is often a large deformation part of die forging processing, and the accumulated strain energy is easy to excite a coarse-grained structure, which brings a serious challenge to the alloy design and processing technology of products.
Patent CN106350708A proposes a preparation method for inhibiting coarse grain rings of aluminum alloy extruded bars for automobile control arms, which realizes the structure control of extruded bars by controlling the content of alloy elements, extruding dies and adjusting the process. Patent CN102644039A provides a preparation method of a high-quality 6061 aluminum alloy forging for semiconductor equipment, and the purpose of controlling the texture structure of the forging is realized by adjusting the forging process parameters and controlling the temperature field and the stress field of the forging. Patent CN109609882A proposes a method for reducing the depth of a coarse grain layer on the surface of an aluminum alloy hot forging, which aims to eliminate the coarse grain structure on the surface of the forging by adding local cold plastic deformation and cold finishing procedures of the surface metal of a forging stock in the conventional aluminum alloy hot forging procedure.
Literature research and patent analysis show that the traditional control process of the coarse grain structure of the aluminum alloy die forging piece usually needs to additionally apply special processing deformation or needs to strictly limit the parameters of the extrusion and forging processes, and the industrial adaptability is low. And the process is longer in the die forging forming process, the accumulated stress energy of thermal deformation of each process is higher, and the deformation of the reinforcing rib part of the structural member can not be sacrificed in order to ensure the mechanical property, so that the control of the coarse grain structure is difficult, the control effect which is considered in two aspects is difficult to achieve in the industrial production link, and the scrapping of batch products or the failure of part of key structural parts to meet the harsh anti-fatigue requirements of vehicle load conditions are caused.
Disclosure of Invention
The technical problem to be solved by the invention is as follows: the invention provides a preparation method of an Al-Mg-Si series aluminum alloy die forging for inhibiting a coarse grain structure, aiming at the problems that the aluminum alloy die forging has large deformation amount and high accumulated deformation energy and is easy to have the coarse grain structure.
The Al-Mg-Si series aluminum alloy adopted by the invention comprises the following alloy elements in percentage by mass: 0.4 to 1.5 percent of Mg, 0.3 to 1.5 percent of Si, 0.01 to 0.7 percent of Cu, 0.01 to 0.3 percent of Fe, 0.01 to 1.0 percent of Mn, 0.001 to 0.25 percent of Zr, 0.01 to 0.5 percent of Cr, 0.001 to 0.25 percent of Sc, 0.01 to 0.1 percent of V, 0.01 to 0.25 percent of Ti and other undefined transition elements with the content of less than 0.1 percent, and the balance of Al and inevitable impurities, wherein the precipitated particles of the transition elements have the functions of obviously inhibiting the generation and the growth of coarse crystals, the sum of the total mass contents of all the transition elements except the Fe element is controlled to be between 0.24 and 1.19 percent, and the sum of [ Fe ]% +1.1[ Mn ] is less than or equal to 0.7 percent and the sum of [ Mn ]% and 3[ Cr ] is less than or equal to 1.05 percent. The content of inevitable impurities is 0.04% or less, and the total content of inevitable impurities is 0.18% or less.
The invention provides a preparation method of a die forging of Al-Mg-Si series aluminum alloy for inhibiting coarse grain structure, which comprises the following steps:
firstly, melt cleaning treatment: and putting an aluminum ingot or electrolytic aluminum liquid into a smelting furnace for melting treatment, wherein the heating temperature of the aluminum liquid ranges from 730 ℃ to 780 ℃, an aluminum-based intermediate alloy and a pure metal ingot are respectively added according to the calculated addition amount, and a magnesium ingot is pressed in a cage type and is immersed below the liquid level of the melt until the magnesium ingot is completely melted so as to prevent burning loss and oxide inclusions from being involved. Fully stirring after the completion to ensure that the components of the aluminum liquid are uniform. And refining the melt for 1-3 times at the temperature of 720-740 ℃ by adopting a granular flux and high-purity argon with the content of more than 99.7 percent, wherein the refining time of a single time is 30-40 minutes, and after the refining is finished, the melt is subjected to slag skimming and is kept stand for 30-60 minutes, so that fine inclusions and non-fusible impurity particles in the melt have sufficient time to float and sink. After standing, the aluminum alloy melt is subjected to online refining, double-rotor degassing and 30PPi/50 PPi or 40PPi/60PPi double-stage filtration treatment, and then is subjected to semi-continuous casting. Al-Ti-B or Al-Ti-C wire type alloys can be used as the refiner for online refining, and several alloys are selected for application in specific embodiments. The gas source gas for the double-rotor degassing is high-purity argon with the content of more than 99.7 percent.
Secondly, semi-continuous casting: and (3) preparing the ingot into a die forging blank by adopting a vertical semi-continuous casting mode of a plurality of near-forging hot top type crystallizers with rapid cooling and cross section shapes close to the projection size of the die forging, wherein the ratio of the cross section area of the ingot to the projection area of the die forging is 0.85-1.18. The casting crystallizer is independently designed with a lubricating oil cavity and a cooling water cavity, continuous online oil lubrication and water spray cooling are carried out on the ingot by the crystallizer in the casting process, the temperature of a melt is controlled to be 680-720 ℃, the cooling rate of the center of the ingot is 5-80 ℃/s, the total thickness of a segregation layer on the surface of the ingot and a chilling layer is smaller than 1.6mm, the outer surface of the ingot is smooth, and the internal structure is compact. And after the casting is finished, sawing the cast ingot into laminar blanks with the thickness of 10 mm-60 mm along the vertical casting direction for subsequent die forging forming.
Thirdly, multi-stage speed control homogenization: in order to ensure that transition group elements which are forcibly dissolved in crystal grains under the semi-continuous casting condition are uniformly dispersed and precipitated and eutectic strengthening phases distributed in crystal boundaries are fully dissolved, lamellar forging stocks are alternately placed in an air circulating furnace, and homogenization treatment is carried out by adopting the processes of slow temperature rise, multi-stage homogenization and controlled cooling. Heating the forging stock to a first-stage homogenizing temperature of 300-420 ℃ at room temperature at a heating rate of 50-100 ℃/h, and preserving heat for 4-8 h, wherein the temperature range is the dispersion precipitation temperature of the transition compound. The second-stage temperature range is 480-510 ℃, and the heating rate is as follows: 150-300 ℃/h and the heat preservation time is 3-10 h. The third-stage temperature range is 540-580 ℃, and the heating rate is as follows: 150-300 ℃/h and the heat preservation time is 5-15 h. The second-stage homogenization setting temperature and the third-stage homogenization setting temperature are both Al in the alloy2Cu phase and Mg2The dissolution and re-dissolution temperature of the Si phase, if the Cu content in the alloy is less than 0.1%, the second-stage temperature range can be not set. Are all made ofAfter the quality treatment is finished, the forging stock is cooled to room temperature in a mode of controlling the cooling speed to be between 100 ℃/h and 300 ℃/h, and after the homogenization is finished, transition group particles in the crystal grains are uniformly dispersed and separated out, wherein the size range is between 20 nm and 50 nm.
Fourthly, die forging forming at room temperature or high temperature: and (3) carrying out die forging deformation for 1-3 times after the homogenized lamellar blank is subjected to heat preservation for 2-10 hours at room temperature or heated to 320-420 ℃, wherein the heating temperature of a die is as follows: 280-400 ℃. In order to ensure the requirements of mechanical property and fatigue durability of the die forging, the accumulated machining deformation of the metal blank at the bearing position of the forging in the X direction, the Y direction or the Z direction is more than 55 percent, a segregation layer on the peripheral surface of the forging blank uniformly and completely flows to the outer side of the body, the forging is subjected to pressing, remaining and trimming treatment after die forging to obtain a non-defective forging, and the residue of trimmed edges is less than 2 mm.
Fifthly, two-stage solid solution and aging: and performing heat treatment on the die forging piece in a mode of matching two-stage solid solution with one-stage or two-stage aging so as to ensure the requirements on the structure and the performance of the die forging piece. In order to release strain energy storage accumulated in forging deformation, a two-stage solution treatment process is adopted, the first-stage solution temperature is controlled to be 300-470 ℃, the heating rate is 70-200 ℃/h, the heat preservation time is 2-4 h, the first-stage solution temperature is lower than the recrystallization temperature of the alloy, and the die forging piece only has a recovery process to release energy storage in the temperature range, but does not have recrystallization. The second-stage solid solution temperature is the solid solution temperature of the strengthening phase particles, the temperature range is 530-570 ℃, the temperature rise rate is 100-300 ℃/h, the heat preservation time is 2-6 h, and the strengthening phase particles are completely solid-dissolved in the crystal grains within the temperature range to form a single-phase solid solution. The forging after the solution treatment is placed in cooling water at 25-80 ℃ for quenching treatment within 30s at the maximum time, is placed for 2-48 h and then is subjected to single-stage or double-stage aging heat treatment under the condition of heat preservation at 150-260 ℃ for 6-20 h, and is subjected to air cooling after the aging is completed.
In the implementation method, the microscopic morphology of the section of the force-bearing part of the aluminum alloy die forging is a fiber deformation structure along a deformation streamline, no coarse grains or coarse grain structure characteristics exist, the thickness of the coarse grain layer on the surface of the forging is less than or equal to 1mm, and the yield strength is 300-410 MPa; the tensile strength is 350-440 MPa; the elongation percentage is 10-16%, the anti-fatigue and anodic oxidation performance is excellent, and the aluminum alloy can be applied to aluminum alloy structural members of vehicle transportation and transport tools to replace steel parts to achieve light weight and weight reduction effects.
The invention has the beneficial technical effects that: (1) the Al-Mg-Si series aluminum alloy adopted by the invention limits the content of strengthening elements in the alloy, limits the single content and the total content of transition group elements such as Fe, Mn, Zr, Cr, Ti, V, Sc and the like and impurity elements, ensures that the particles do not form harmful phases and can separate out a sufficient number of dispersed particles which play a role in limiting the growth of coarse crystals in the homogenizing process, inhibits the coarse crystal structure of an Al-Mg-Si series aluminum alloy forging from the aspects of alloy design and selection, and expands the variety selection range of the aluminum alloy structural member for vehicles. (2) According to the semi-continuous casting method, the near-forging section ingot is adopted for semi-continuous casting, the ingot is directly prepared after being sawed into slices and subjected to a multi-stage speed control homogenization process, the mode that the forging blank is prepared after the semi-continuous casting round ingot is subjected to homogenization extrusion deformation in the traditional process is abandoned, the defects of high strain energy storage and high probability of appearance of coarse grain tissues caused by die forging by adopting an extrusion ingot in the traditional process can be effectively overcome, and the strain energy storage is remarkably reduced by the novel process. (3) The semi-continuous ingot casting method adopts a speed-control multistage homogenization treatment process, can ensure that the precipitation size of the dispersed particles of the transition group is fine, dispersed and sufficient, and realizes the coarse grain structure inhibition of the die forging through component control and precipitation particle size control. (4) The heat treatment of the die forging adopts a two-stage solid solution cooperation aging system, and compared with the traditional process, the recovery and stress release treatment temperature of the first-stage die forging is increased, the phenomenon that the die forging is directly heated to a high-temperature solid solution temperature, the recrystallization is stimulated by high internal energy storage and abnormal growth is caused in the traditional process is effectively prevented, and the flow line forging tissue characteristics are reserved at the high-bearing-capacity deformation part of the forging, so that the product has high strength and toughness, and good fatigue resistance and anodic oxidation resistance.
Detailed Description
The following description of the preferred embodiments of the present invention is provided for the purpose of illustration and description, and is in no way intended to limit the invention.
Example 1
An Al-Mg-Si series aluminum alloy for inhibiting a coarse grain structure, which comprises the following components: 0.9% of Mg, 1.0% of Si, 0.19% of Cu, 0.21% of Fe, 0.11% of Mn, 0.001% of Zr, 0.20% of Cr, 0.001% of Sc, 0.011% of V, 0.16% of Ti and other undefined transition group elements with a content of less than 0.1%, the balance being Al and unavoidable impurities, the sum of the total contents of all the transition group elements except Fe being controlled to be 0.48% to 0.51%, and [ Fe ]% +1.1[ Mn ]% < 0.33%, [ Mn ] +3[ Cr ] < 0.71%, the contents of the other unavoidable impurity elements being less than 0.02%, while the total content of the unavoidable impurity elements being less than 0.09%.
The preparation method of the alloy die forging comprises the following steps:
and putting the weighed industrial pure aluminum ingot into a smelting furnace for melting treatment, heating the aluminum liquid to 730-740 ℃, respectively adding aluminum-based intermediate alloy into the melt according to the calculated addition amount, and pressing and immersing the pure magnesium ingot in a cage type until the pure magnesium ingot is completely melted until the pure magnesium ingot is burnt and oxidized in the adding process of the magnesium ingot. Fully stirring after the addition is finished to ensure that the components of the aluminum liquid are uniform. And refining the aluminum alloy melt for 2 times at the melt temperature of 720-740 ℃ by adopting a granular sodium-free refining agent and high-purity argon with the purity of 99.7 percent, wherein the refining time is 30 minutes each time. And after refining, slagging off the melt and standing for 40 minutes to ensure that fine inclusions fully float and sink to clean the melt. After standing, an Al-5Ti-1B refiner is adopted, and the melt is subjected to double-rotor degassing and 30PPi/50 PPi double-stage filtration treatment and then semi-continuous casting is carried out.
The method comprises the steps of vertically and semi-continuously casting a forging blank by using a hot top type crystallizer with the cross section shape close to that of a forging piece, wherein the ratio of the cross section area of an ingot to the projection area of a final die forging piece is 1.06, 6 ingots are cast in the same level in each furnace, the temperature of a melt before entering a casting disc is 690-700 ℃, a crystallizer applies continuous oil lubrication and water spray cooling to the surface of the ingot in the casting process, an embedded thermocouple is used for detecting that the cooling rate of the central part of the ingot is 25 ℃/s, the fastest cooling rate of the edge part is 270 ℃/s, and the total thickness of a segregation layer on the surface of the ingot blank and a chilling layer is 0.6 mm. After the semi-continuous casting is finished, the sheet-shaped blank with the thickness of 26mm is sawed along the vertical casting direction.
In order to ensure that the blank is fully homogenized and transition group particles are fully dispersed and separated out, the forging stocks are alternately placed in an air circulating furnace at intervals, heated to the first-stage homogenization temperature of 360 ℃ at the room temperature at the speed of 100 ℃/h, kept warm for 6h, continuously heated to the second-stage homogenization temperature of 490 ℃ at the speed of 250 ℃/h, kept warm for 3h, heated to the third-stage homogenization temperature of 560 ℃ at the heating speed of 300 ℃/h, and kept warm for 12 h. Then immediately cooling to room temperature at a rate of 230 ℃/h, and carrying out semi-continuous casting on Al formed at grain boundaries in the ingot blank in the homogenization process2Cu phase and Mg2The Si phase is fully dissolved, and the precipitation size of transition group element particles in the crystal grains is between 20 and 50 nm.
And (3) carrying out die forging forming on the homogenized lamellar forging stock in a heating state, wherein the heating temperature of the stock is 390 ℃, the heat preservation is carried out for 3 hours, the heating temperature of a die is 300 ℃, and the finished product is obtained after 2 times of pre-forging and finish forging die forging deformation. And (2) performing die forging deformation for the 1 st time, wherein an element segregation layer on the periphery of the forging blank uniformly flows to the outer side of the forging blank under the action of pressure, the deformation of the product bearing metal blank in the X direction, the Y direction or the Z direction is more than 20%, the blank is taken out from a pre-forging die after die forging is completed and is directly subjected to finish forging forming, the deformation of the forging blank at the stage is more than 40%, all forging flashes are extruded to the outer side of the forging blank, trimming is performed on the forging by using a trimming die after 2 times of die forging, and the residue of trimmed burrs is less than 1mm, so that the defect-free forging is obtained.
The forging is subjected to heat treatment by adopting a two-stage solid solution matched single-stage aging system, the temperature of the forging is increased to 320 ℃ from room temperature at the heating rate of 100 ℃/h in the solid solution process and is kept for 3h, the temperature of the forging is increased to 550 ℃ from the second-stage solid solution temperature at the heating rate of 250 ℃/h after the first-stage solid solution process is finished and is kept for 4h, after the strengthening phase particles are completely dissolved, the forging after quenching treatment is immediately and rapidly placed in cooling water at the temperature of 30 ℃ within 20s for quenching treatment, the forging after quenching treatment is placed in an aging furnace set to 180 ℃ within 48h for treatment for 12h, and the forging is air-cooled to room temperature after being taken out of the furnace.
After the aluminum alloy die forging is prepared, the cross-section structure of the forging is detected, the shape of the cross-section structure of the bearing position of the forging is a fiber deformation structure along the forging flow line, no coarse grain structure or coarse grain structure characteristic is found, a mechanical property test sample is selected from the position of a reinforcing rib of the die forging, and the yield strength is 320-350 MPa; the tensile strength is 380-400 MPa; the elongation is 11-13%, and the anti-fatigue and surface anodic oxidation properties are excellent.
Example 2
An Al-Mg-Si series aluminum alloy die forging piece is eliminated, and the alloy comprises the following components: 0.8% of Mg, 1.3% of Si, 0.09% of Cu, 0.11% of Fe, 0.45% of Mn, 0.15% of Zr, 0.12% of Cr, 0.08% of Sc, 0.02% of V, 0.07% of Ti and other undefined transition group elements with a content of less than 0.1%, the balance being Al and unavoidable impurities, the sum of the total contents of all the transition group elements except Fe being controlled to be 0.79% to 0.82%, and [ Fe ]% +1.1[ Mn ]% is less than or equal to 0.61%, and [ Mn ]% +3[ Cr ]% is less than or equal to 0.81%, the contents of the other unavoidable impurity elements are less than 0.03%, and the total content of the unavoidable impurity elements is less than 0.12%.
The preparation method of the alloy die forging comprises the following steps:
and putting the weighed industrial pure aluminum ingot into a smelting furnace for melting treatment, heating the aluminum liquid to 740-750 ℃, respectively adding aluminum-based intermediate alloy into the melt according to the calculated addition amount, pressing the pure metal magnesium ingot in a cage mode to prevent oxidation and burning loss, and fully stirring to ensure that the components of the aluminum liquid are uniform. And refining the aluminum alloy melt for 3 times at the melt temperature of 730 ℃ by adopting a sodium-free particle refining agent and high-purity argon with the purity of 99.8 percent, wherein the refining time is 20 minutes each time. And after refining, slagging off and standing for 30 minutes to ensure that fine inclusions float and sink sufficiently. After standing treatment, the alloy melt is refined on line by adopting Al-3Ti-0.2B wires, and semi-continuous casting is carried out after double-rotor degassing and 40ppi/60ppi double-stage filtration respectively.
The method comprises the steps of adopting a hot top type crystallizer with a near forging cross section shape to semi-continuously cast a forging blank, enabling the ratio of the cross section area of an ingot to the projection area of a final die forging to be 1.21, casting 4 ingots in the same level in each furnace, enabling the temperature of a melt before entering a casting disc to be 700-705 ℃, enabling a crystallizer to apply continuous oil lubrication and water spray cooling to the surface of the ingot in the casting process, detecting the cooling rate of 50 ℃/s at the central part of the ingot by adopting an embedded thermocouple, enabling the cooling rate of the edge part to be 360 ℃/s at the fastest speed, and enabling the total thickness of a segregation layer and a chilling layer on the surface of the ingot to be 1.1 mm. After the semi-continuous casting is finished, the sheet-shaped blank with the thickness of 23mm is sawed along the vertical casting direction.
The method comprises the steps of carrying out semi-continuous casting in the vertical direction by adopting 4 symmetrically-arranged hot top type crystallizers, wherein the temperature of a melt before casting is 700-710 ℃, carrying out semi-continuous casting and forming after an ingot is subjected to oil lubrication on the surface of the crystallizer and chilling by cooling water, detecting the cooling rate in the ingot by adopting an immersion thermocouple, wherein the central part is 45 ℃/s, the cooling position is 260 ℃/s, the total thickness of a segregation layer on the surface of the ingot and the chilling layer is 1.2mm, and the ratio of the sectional area of the ingot to the projection area of a die forging is 1.21. After the semi-continuous casting is finished, the sheet-shaped blank with the thickness of 23mm is sawed.
In order to ensure that the blank is fully homogenized and simultaneously promote the transition group particles to be fully dispersed and separated out, the forging stocks are alternately placed and heated to the first-stage homogenization temperature of 420 ℃ from the room temperature of 30 ℃ at the speed of 80 ℃/h in an air circulation furnace, the temperature is kept for 6h, then the forging stocks are continuously heated to the third-stage homogenization temperature of 565 ℃ at the speed of 200 ℃/h, and the temperature is kept for 12 h. Cooling the high-temperature ingot blank to room temperature at the speed of 230 ℃/h immediately after the homogenization treatment is finished, wherein Mg in the ingot blank is in the process of the stage2The Si phase is fully dissolved, and the precipitation size of transition group element particles in the crystal grains is between 30 and 50 nm.
And die forging the homogenized lamellar blank in a heating state, heating the blank to 400 ℃, keeping the temperature for 3 hours, then carrying out die forging, heating the die to 330 ℃, carrying out continuous 2-time die forging deformation on the blank to obtain a finished product, wherein the accumulated deformation of the main bearing part X, Y or the Z direction of the forge piece is more than 65%, the peripheral segregation layer of the forge piece is completely extruded to the outer side of the body in the die forging deformation process and is completely cut off by a trimming die, and the burr residual of the forge piece after being cut is 0.8 mm.
And (3) carrying out heat treatment on the forged piece by adopting a two-stage solid solution process and a single-stage aging system. And in the solution treatment stage, the temperature of the forge piece is increased from room temperature to the first-stage solution temperature of 340 ℃ at the heating rate of 100 ℃/h and is kept for 2h, so that the thermal deformation strain energy accumulated in the die forging process is released. After heat preservation, the temperature is continuously increased from 340 ℃ to 560 ℃ of the second-stage solid solution temperature at the heating rate of 250 ℃/h, and heat preservation is carried out for 5h, and strengthening phase particles are solid-dissolved in the crystal at the stage so as to be precipitated in subsequent aging strengthening. And (3) placing the forging subjected to the solution treatment in cooling water of 25 ℃ for 20s for quenching, placing the forging subjected to the quenching treatment in an aging furnace of 190 ℃ for 10h within 48h, and discharging and cooling the forging to room temperature by air.
After the aluminum alloy die forging is prepared, the cross section of the bearing part of the forging is detected by corrosion, the characteristics of coarse grain structure and coarse recrystallization structure are not found, and the cross section structure is all fibrous structure along the forging streamline due to the fact that the aluminum alloy die forging contains higher transition group elements. Selecting a part of the die forging with the section thickness exceeding 10mm for mechanical property test, wherein the yield strength is 350-390 MPa; the tensile strength is 410-430 MPa; the elongation is 10-12%, and the anti-fatigue and surface anodic oxidation properties are excellent.
Example 3
The method for eliminating the coarse grain structure of the Al-Mg-Si series aluminum alloy die forging comprises the following components in percentage by weight: 0.8% of Mg, 0.7% of Si, 0.09% of Cu, 0.13% of Fe, 0.4% of Mn, 0.15% of Zr, 0.16% of Cr, 0.012% of Sc, 0.02% of V, 0.06% of Ti and other undefined transition group elements with a content of less than 0.1%, the balance being Al and unavoidable impurities, the sum of the total contents of all the transition group elements except Fe being controlled to be 0.85% to 0.91%, and [ Fe ]% +1.1[ Mn ]% is less than or equal to 0.57%, [ Mn ] +3[ Cr ]% is less than or equal to 0.88%, the contents of the other unavoidable impurity elements are less than 0.02%, and the total content of the unavoidable impurity elements is less than 0.08%.
The preparation method of the alloy die forging comprises the following steps:
according to the component requirements of the embodiment, electrolytic aluminum liquid and aluminum-based intermediate alloy are put into a smelting furnace for smelting, the temperature of the aluminum liquid is controlled to be 750-760 ℃, pure metal magnesium ingots are pressed into the smelting furnace in a cage mode and immersed below the liquid level of the melt until the pure metal magnesium ingots are completely molten, and the molten aluminum is fully stirred after the smelting is finished, so that the components of the aluminum liquid are uniform. Controlling the temperature of the melt at 730-740 ℃ for refining, and refining the melt for 2 times by adopting a granular sodium-free flux and high-purity argon with the purity of 99.8%, wherein the refining time is 35 minutes each time. And after refining, slagging off the melt and standing for 40 minutes to ensure that fine inclusions fully float and sink to clean the melt. After standing, the melt is refined by an online Al-5Ti-0.3C wire, and semi-continuous casting is carried out after double-rotor degassing and 30PPi/50 PPi double-stage filtration respectively.
The method comprises the steps of preparing a forging blank by adopting 6 symmetrically-arranged hot-top crystallizers in a vertical semi-continuous casting mode, wherein the ratio of the cross section area of the forging blank to the projection area of a final die forging is 1.09, the crystallizers apply continuous oil lubrication and water spray cooling to the surface of an ingot in the casting process, the temperature of a melt before entering a casting disc is 690-710 ℃, an embedded thermocouple is adopted to detect the cooling rate of the central part of the ingot to be 30 ℃/s, the fastest cooling rate of the edge part to be 280 ℃/s, and the total thickness of a segregation layer on the surface of the ingot and a chilling layer to be 1.3 mm. And after the semi-continuous casting is finished, sawing the semi-continuous casting into sheet-shaped blanks with the thickness of 23mm along the vertical casting direction for die forging forming.
In order to ensure that the blank is fully homogenized and simultaneously ensure the dispersion precipitation of transition group particles, forging stock slices are placed at intervals in an air circulation furnace and subjected to speed-controlled graded homogenization heat treatment, the forging stock is heated from room temperature to 390 ℃ of a first-stage homogenization temperature at the heating rate of 70 ℃/h and is kept warm for 6h, then the forging stock is continuously heated to 460 ℃ of a second-stage homogenization temperature at the heating rate of 200 ℃/h and is kept warm for 4h, then the forging stock is heated to 550 ℃ of a third-stage homogenization temperature at the heating rate of 300 ℃/h and is kept warm for 10h, and the strengthening eutectic phase is fully dissolved in the homogenization process. After homogenization the billet slices were immediately cooled to room temperature at a rate of 260 ℃/h. Mg in the forged blank during this stage2The Si phase is fully dissolved, and the precipitation size of the intragranular transition group element particles is 30-50 nm.
And performing die forging deformation on the forged blank after the homogenization treatment in a hot state, heating the blank to 400 ℃, keeping the temperature for 4 hours, heating the die to 330 ℃, performing 2 times of continuous die forging forming on the forged blank in the hot state, wherein the accumulated deformation of the bearing position of the forged piece in the X direction, the Y direction or the Z direction is 75%, the forging fins are all extruded to the periphery of the body in the deformation process, and trimming is performed on the finished product by using a trimming die to obtain the defect-free forged piece, wherein the residual quantity of the burrs is less than 1 mm.
And finishing the heat treatment process of the die forging by adopting a two-stage solid solution process and an aging system. And in the solid solution treatment stage, the forging is heated from room temperature to a primary solid solution temperature of 380 ℃ at the heating rate of 100 ℃/h and is kept warm for 2h to release strain energy storage in the forging forming stage, then the temperature is continuously increased to a secondary solid solution temperature of 555 ℃ at the heating rate of 250 ℃/h and is kept warm for 5h, the forging after the solid solution treatment is placed in cooling water for quenching treatment in 20s, and the temperature of the quenching cooling water is 25 ℃. And (3) placing the quenched forging in 48h at 200 ℃ for heat preservation for 10h for aging heat treatment, discharging the forging after the aging is finished, and air-cooling to room temperature.
According to the embodiment, the microscopic morphology of the section of the force bearing part of the aluminum alloy die forging is a fiber deformation structure along a deformation streamline, no coarse grains and coarse grain structures exist, the thickness of the coarse grain layer on the surface of the forging is 0.8mm, and the yield strength is 355-380 MPa; the tensile strength is 390-420 MPa; the elongation percentage is 10-13%, the anti-fatigue and anodic oxidation performance is excellent, and the aluminum alloy can be applied to aluminum alloy structural members of vehicles and transport tools.
Example 4
An Al-Mg-Si series aluminum alloy for inhibiting a coarse grain structure, which comprises the following components in percentage by weight: 0.5% of Mg, 0.65% of Si, 0.09% of Cu, 0.17% of Fe, 0.35% of Mn, 0.19% of Cr, 0.002% of Sc, 0.08% of V, 0.06% of Ti and other undefined transition group elements with the content of less than 0.1%, the balance being Al and inevitable impurities, the sum of the total content of all the transition group elements except the Fe element is controlled between 0.59% and 0.62%, and [ Fe ]% +1.1[ Mn ]% < 0.56%, [ Mn ]% +3[ Cr ]% < 0.92%, the content of the other inevitable impurities is less than 0.02%, and the total content of the inevitable impurities is less than 0.07%.
The preparation method of the alloy die forging comprises the following steps:
and (2) putting the weighed electrolytic aluminum liquid, aluminum-based intermediate alloy and 30% of returning charge into a smelting furnace for melting treatment, heating the aluminum liquid to 730-740 ℃, pressing in pure metal magnesium ingots in a cage mode according to the calculated addition amount, and fully stirring to ensure that the components of the aluminum liquid are uniform. The melt temperature is in the range of 720-730 ℃, and the aluminum melt is refined for 2 times by adopting a sodium-free refining agent and high-purity argon with the content of more than 99.7 percent, wherein the refining time is 35 minutes each time. And after refining, the melt is subjected to slag skimming and standing treatment for 40 minutes, so that fine inclusions and non-fusible impurity particles in the melt can float and sink in sufficient time. Al-5Ti-1B wire is adopted to refine melt on line, and semi-continuous casting is carried out after double-rotor degassing and 30PPi/50 PPi double-stage filtration respectively.
5 hot top type crystallizers which are arranged in central symmetry are used as alloy casting die discs, and a vertical semi-continuous casting mode is applied to prepare die forging blanks. The temperature of the melt subjected to degassing and filtering before entering the casting tray is 695-705 ℃, the crystallizer continuously applies oil lubrication and water spray cooling to the cast ingot through a lubricating oil cavity and a cooling water cavity respectively, and the ratio of the sectional area of the cast ingot to the projection area of the final die forging product is controlled to be 1.21. The embedded thermocouple is adopted to detect that the cooling rate of the central part of the cast ingot is 50 ℃/s, the cooling rate of the edge part is 230 ℃/s, the total thickness of the segregation layer and the chilling layer on the surface of the cast ingot is 1.3mm in an online manner, and the cast ingot is cut into forging stock slices with the thickness of 21mm after casting.
The forging stock is prepared by adopting a semi-continuous casting mode of 6 same-level hot tops with quick cooling and the section shape close to the projection size of the die forging, and the ratio of the ingot casting section area to the die forging projection area is 0.95. The hot top type casting crystallizer adopts the independent design of a lubricating oil cavity and a cooling water cavity, and the cast ingot is subjected to online continuous oil lubrication and water spray cooling in the casting process. The temperature of the melt before entering the casting disc is controlled to be 700-710 ℃, the cooling rate of the center of the cast ingot is 45 ℃/s, the total thickness of the segregation layer and the chilling layer on the surface of the cast ingot is 0.8mm, the outer surface of the cast ingot is smooth, and the internal structure is compact. After casting, the ingot was sawed into a 20mm thick sheet-like forged blank in the vertical casting direction.
The forging stock slices are placed in an air circulating furnace at intervals for multi-stage speed-control homogenization treatment, the forging stock is heated from room temperature to the first-stage homogenization temperature of 420 ℃ at the heating rate of 50 ℃/h at the heating rate of 100 ℃/h and is kept warm for 5h, then the forging stock is continuously heated to the second-stage homogenization temperature of 480 ℃ at the heating rate of 250 ℃/h and is kept warm for 4h, and then the forging stock slices are heated to the third-stage homogenization temperature of 560 ℃ at the heating rate of 300 ℃/h and are kept warm for 10 h. After the homogenization treatment is finished, the high-temperature forging stock slices are immediately cooled to room temperature at the speed of 100 ℃/h. After homogenization, transition group particles in the crystal grains are uniformly dispersed and separated out, and the size range is 20-50 nm.
And (2) forming the homogenized forging stock at room temperature, wherein the heating temperature of the die is 330 ℃, in the 1 st die forging forming process, the deformation of the metal stock in the X direction, the Y direction or the Z direction is more than 15%, a peripheral element segregation layer of the stock uniformly flows to the outer side of the body, the blank is taken out from the die to be directly subjected to the 2 nd die forging after the die forging is completed, the temperature of the body of the blank is increased under the heat of deformation and the heating of the die at the stage, the structural structure is subjected to deformation refining in the 1 st die forging, and the integral plasticity is improved. In the 2 nd die forging deformation, the deformation of the force bearing position of the die forging piece is more than 45 percent, and no cracking occurs. The blank segregation layer and the forging flash are all extruded to the outer side of the body in the deformation process, the trimming die is adopted to perform trimming processing on the forged piece finished product, and the residual quantity of the trimmed flash is smaller than 1 mm.
And (3) adopting a two-stage solid solution process and an aging system to implement the heat treatment process of the die forging. Controlling the first-stage solid solution temperature of the forge piece to be 450 ℃, the heating rate to be 80 ℃/h and the heat preservation time to be 3h, releasing die forging strain energy storage at the stage, then continuously heating to the second-stage solid solution temperature of 560 ℃ at the heating rate to be 300 ℃/h, preserving heat for 5h for solid solution treatment, and then putting the high-temperature forge piece into cooling water at 25 ℃ within 20s for quenching treatment. And after the forging is placed for 48 hours, placing the forging in an aging furnace at 190 ℃ for heat preservation for 8 hours for aging treatment, and discharging the forging and cooling the forging to room temperature by air.
In the implementation method, the microscopic morphology of the section of the force-bearing part of the aluminum alloy die forging is a fibrous structure along a deformation streamline, no coarse grains or coarse grain structure characteristics exist, the thickness of the coarse grain layer on the surface of the forging is less than or equal to 0.7mm, and the yield strength is 310-350 MPa; the tensile strength is 370-400 MPa; the elongation is 11-15%, and the anti-fatigue and anodic oxidation properties are excellent.
Claims (5)
1. The preparation method of the die forging of the Al-Mg-Si series aluminum alloy for inhibiting the coarse grain structure is characterized in that the Al-Mg-Si series aluminum alloy comprises the following components in percentage by mass: 0.4 to 1.5 percent of Mg0.3 to 1.5 percent of Si0.3 to 1.5 percent of Cu0.01 to 0.7 percent of Cu0.01 to 0.3 percent of Fe0.01 to 0.3 percent of Mn0.01 to 1.0 percent of Zr0.001 to 0.25 percent of Cr0.01 to 0.5 percent of Sc0.001 to 0.25 percent of V0.01 to 0.1 percent of Ti0.01 to 0.25 percent of other transition group elements with the content of less than 0.1 percent which are not limited, and the balance of Al and inevitable impurities; the total mass content of all transition elements except Fe in the aluminum alloy is between 0.24% and 1.19%, and [ Fe ]% +1.1[ Mn ]% is less than or equal to 0.7%, and [ Mn ]% +3[ Cr ]% is less than or equal to 1.05%; the content of inevitable impurities is less than or equal to 0.04 percent, and the total content of inevitable impurities is less than or equal to 0.18 percent;
the die forging is prepared by the following process steps:
firstly, melt cleaning treatment: putting an aluminum ingot or electrolytic aluminum liquid into a smelting furnace, preparing an alloy according to the mass fraction of each element required by the components, heating the aluminum ingot or the electrolytic aluminum liquid to 730-780 ℃, adding alloy elements in an intermediate alloy mode, pressing a magnesium ingot in a cage mode, carrying out refining treatment for 1-3 times at the melt temperature of 720-740 ℃ after complete melting, wherein the time of each time is 30-40 minutes, standing for 30-60 minutes after refining is finished, and carrying out semi-continuous casting after online refining, double-rotor degassing and two-stage filtration treatment;
secondly, semi-continuous casting: preparing die forging blanks from the cast ingots by adopting a vertical semi-continuous casting mode of a plurality of near-forging hot top crystallizers; in the casting process, the crystallizer continuously applies lubricating oil and sprays water for cooling the ingot, and the casting temperature is between 680 and 720 ℃; the area ratio of the cross section of the cast ingot to the die forging piece is 0.85-1.18, and after casting is finished, the cast ingot is sawed into lamellar blanks with the thickness of 10-60 mm along the vertical casting direction;
thirdly, multi-stage speed control homogenization: the die forging blank is treated by adopting a grading speed-control homogenizing process in an air circulating furnace, and the temperature range of the first-stage homogenizing treatment is as follows: 300-420 ℃, and the heating rate of the ingot from room temperature 25 ℃ to the first-stage temperature is as follows: 50-100 ℃/h, and the heat preservation time is 4-8 h; the second-stage temperature range is 480-510 ℃, and the heating rate is as follows: 150-300 ℃/h, and the heat preservation time is 3-10 h; the third-stage temperature range is 540-580 ℃, and the heating rate is as follows: 150-300 ℃/h, and the heat preservation time is 5-15 h; after the multistage homogenization is finished, cooling the die forging blank to room temperature by adopting a mode of controlling the cooling speed to be between 100 ℃/h and 300 ℃/h; after the multi-stage speed control homogenization is completed, the precipitation size of transition group particles in crystal grains of the die forging blank is 20-50 nm;
fourthly, die forging forming at room temperature or high temperature: the forging blank after the multistage speed control homogenization treatment is subjected to die forging molding for 1-3 times after being kept at room temperature or heated to 320-420 ℃ for 2-10 hours, and the heating temperature range of the die is as follows: 280-400 ℃, wherein the accumulated machining deformation of the blank in the X direction, the Y direction or the Z direction is more than 55 percent in the die forging process;
fifthly, two-stage solid solution and aging: performing strengthening and toughening heat treatment by adopting a two-stage solid solution matched aging process, putting the forging into cooling water at 25-80 ℃ within 30s after solid solution is completed, performing quenching treatment, standing for 2-48 h, and performing aging heat treatment under the condition of heat preservation at 150-260 ℃ for 6-20 h to obtain a die forging; the two-stage solid solution process comprises the following steps: the temperature range of the first-stage solid solution is 300-470 ℃, the heating rate is 70-200 ℃/h, the heat preservation time is 2-4 h, the temperature range of the second-stage solid solution is 530-570 ℃, the heating rate is 100-300 ℃/h, and the heat preservation time is 2-6 h.
2. The preparation method of the die forging piece according to claim 1, wherein the texture morphology of the force-bearing part of the die forging piece is the fiber deformation texture characteristic along the forging streamline, the thickness of a surface coarse crystal layer is less than or equal to 1mm, and the yield strength of the die forging piece is 300-410 MPa; the tensile strength is 350-440 MPa; the elongation is 10-16%.
3. The preparation method of claim 1, wherein in the first step, the source gas for refining and double-rotor degassing is argon gas with a purity of 99.7% or more, the double-stage filtration adopts 30PPi/50 PPi or 40PPi/60PPi, and the online refining adopts Al-Ti-B wire or Al-Ti-C wire as a refiner.
4. The preparation method according to claim 1, wherein the cooling rate of the ingot in the second step in the central area during water spray cooling is 5 ℃/s to 80 ℃/s, and the total thickness of the surface segregation layer and the chilling layer is less than 1.6 mm.
5. The method according to claim 1, wherein in the fourth step, the surface segregation layer of the forging stock flows to the outer side of the forging body uniformly and completely in the die forging deformation, and the residual quantity of burrs after the die forging cutting is less than 2 mm.
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