WO2011129431A1 - アルミニウム合金鍛造部材の製造方法 - Google Patents

アルミニウム合金鍛造部材の製造方法 Download PDF

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Publication number
WO2011129431A1
WO2011129431A1 PCT/JP2011/059373 JP2011059373W WO2011129431A1 WO 2011129431 A1 WO2011129431 A1 WO 2011129431A1 JP 2011059373 W JP2011059373 W JP 2011059373W WO 2011129431 A1 WO2011129431 A1 WO 2011129431A1
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Prior art keywords
mass
forging
aluminum alloy
forged
forged member
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PCT/JP2011/059373
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English (en)
French (fr)
Japanese (ja)
Inventor
英貴 竹村
寛秋 村上
隆文 中原
美乃里 小林
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昭和電工株式会社
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Priority to JP2012510709A priority Critical patent/JP5756091B2/ja
Priority to CN201180018998.2A priority patent/CN102844456B/zh
Priority to KR1020127026823A priority patent/KR101423412B1/ko
Publication of WO2011129431A1 publication Critical patent/WO2011129431A1/ja

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
    • C22F1/05—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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21J—FORGING; HAMMERING; PRESSING METAL; RIVETING; FORGE FURNACES
    • B21J1/00—Preparing metal stock or similar ancillary operations prior, during or post forging, e.g. heating or cooling
    • B21J1/06—Heating or cooling methods or arrangements specially adapted for performing forging or pressing operations
    • 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
    • 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
    • B21K1/00—Making machine elements
    • B21K1/76—Making machine elements elements not mentioned in one of the preceding groups
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G7/00—Pivoted suspension arms; Accessories thereof
    • B60G7/001—Suspension arms, e.g. constructional features
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/02—Alloys based on aluminium with silicon as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/10—Constructional features of arms
    • B60G2206/11—Constructional features of arms the arm being a radius or track or torque or steering rod or stabiliser end link
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/70—Materials used in suspensions
    • B60G2206/71—Light weight materials
    • B60G2206/7102—Aluminium alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B60—VEHICLES IN GENERAL
    • B60G—VEHICLE SUSPENSION ARRANGEMENTS
    • B60G2206/00—Indexing codes related to the manufacturing of suspensions: constructional features, the materials used, procedures or tools
    • B60G2206/01—Constructional features of suspension elements, e.g. arms, dampers, springs
    • B60G2206/80—Manufacturing procedures
    • B60G2206/81—Shaping
    • B60G2206/8102—Shaping by stamping
    • B60G2206/81022—Shaping by stamping by forging

Definitions

  • the present invention relates to a method for producing an aluminum alloy forged member produced by forging a forged material made of an aluminum alloy to produce a forged member, and a related technique.
  • an aluminum alloy forged member (forged product) is increasingly used as an undercarriage member for automobiles.
  • Al—Mg—Si alloys are often used as alloy materials for such structural aluminum alloy forged members.
  • Non-Patent Document 1 in JIS6061 alloy, which is generally used as an Al—Mg—Si alloy, the material temperature is set to a relatively high temperature of 435 to 480 ° C. in consideration of workability during forging. It is customary to forge.
  • Non-Patent Document 2 As shown in Non-Patent Document 2 below, as an improved Al—Mg—Si alloy in recent years, an alloy whose strength has been improved by suppressing recrystallization during forging (hereinafter referred to as “6000 series high-strength”). "Strength material” has been developed. In order to avoid recrystallization, this alloy is forged at a higher temperature than a general 6061 alloy.
  • Non-Patent Document 1 when a JIS6061 alloy is forged at 435 to 480 ° C., the forging member has a different processing rate for each part depending on its shape, so that the structure state differs depending on each part. End up. For example, an unrecrystallized structure part, a fine recrystallized structure part, and a coarse recrystallized structure part are mixed in one forged member. Thus, if the structure state is different for each part, mechanical characteristics (mechanical strength) such as tensile characteristics (tensile strength) are different for each part, resulting in a forged product having a large variation in mechanical characteristics. .
  • mechanical strength such as tensile characteristics (tensile strength)
  • the mechanical property value that can be guaranteed as a forged product must be set to a value that is significantly lower than the standard test value, and in order to satisfy the guaranteed value of the mechanical property required for structural materials. It is necessary to increase the thickness of the member. As a result, the weight of the forged member is increased, and the weight reduction as the intended purpose is hindered.
  • the non-recrystallized structure is a structure in a state where crystallized matter generated in the final solidified portion exists on the crystal grain boundary in a state where the crystal grains at the time of casting are maintained.
  • the coarse recrystallized structure is a state in which recrystallization occurs with the strain applied by plastic working as a driving force, and the crystal grain size after recrystallization is larger than the crystal grain size during casting. It is.
  • the fine recrystallized structure is a state in which recrystallization occurs with the strain applied by plastic working as the driving force, and the crystal grain size after recrystallization is approximately the same as the crystal grain size during casting. It is an organization that has become or has become smaller.
  • Non-Patent Document 2 can suppress recrystallization in almost the entire area of the forged member in a normal forging process, and also suppress variation in mechanical strength at each part. Can do. However, if a thin-walled forged member is formed in order to reduce the weight, the forging rate will be higher, and the heat dissipation from the forging material during forging will also increase at the thin-walled portion. The temperature decreases and recrystallization easily occurs.
  • the forged member contains an unrecrystallized structure, a coarse recrystallized structure, and a fine recrystallized structure. Therefore, it becomes difficult to obtain an excellent forged product due to the variation in mechanical characteristics. As a result, even if a 6000 series high-strength material is used, it is difficult to reduce the weight as in the case of using the JIS6061 alloy.
  • the present invention has been made in view of the above problems, and a method for producing an aluminum alloy forged member capable of producing a forged member capable of reducing the variation in mechanical properties of each part while reducing the weight, and the method thereof
  • the purpose is to provide related technology.
  • the present inventor conducted experiments and research on the generation behavior of recrystallization during forging, and can control the generation behavior of recrystallization based on the alloy composition of the forging material and the material temperature during forging. I found out.
  • the inventor has found a configuration capable of solving the above-mentioned problems by accurately controlling the occurrence of recrystallization in the forging process and increasing the region of the fine recrystallization structure in the forged member. It came to make.
  • the present invention comprises the following means.
  • the equivalent strain for each part is calculated based on the shape of the forged member to be manufactured and the forging material, and all the equivalent strain for each part is included.
  • the total content of the Fe, Cr, Mn is calculated based on the composition of the forging material, and the forging material temperature is calculated from the total content based on the relational expression.
  • Find the upper limit From the upper limit value of the obtained forging material temperature, based on information relating the forging material temperature prepared in advance and the range of the equivalent strain, the entire equivalent strain range allowed in the forging process is obtained, 3.
  • the method for producing an aluminum alloy forged member according to item 1 or 2 wherein the forged material and the shape of the forged member are designed within the allowable range of equivalent strain.
  • a structural material for an automobile comprising an aluminum alloy forged member manufactured by the manufacturing method according to any one of items 1 to 4.
  • the behavior of recrystallization during forging can be controlled, and a forged member in which a predetermined many regions have a fine recrystallized structure can be obtained.
  • a forged member that is lightweight and excellent in mechanical properties can be obtained.
  • this invention can be used suitably, for example when manufacturing the forge member 10 of the special shape which has a thin part and a thick part as shown in FIG.
  • the forged member 10 includes cylindrical portions 13 and 13 at both ends and a connecting portion 14 that connects both cylindrical portions 13 and 13.
  • the connecting portion 14 has a meat stealing portion 15, and the meat stealing portion 15 is configured as a thin portion 12 having a smaller thickness than the surrounding thick portion 11.
  • the cylindrical parts 13 and 13 are comprised as the thin parts 12 and 12 where the surrounding body part has small thickness.
  • the thickness of the thin portion 12 is 10 mm or less, preferably 10 mm to 3 mm, and the thickness of the thick portion 11 is set to 4 times or more, preferably 4 to 10 times the thickness of the thin portion. It is preferable. Further, for example, when the forged member 10 in FIG. 1 is viewed from above (planar view), the ratio (%) of the area where the thin portion 12 is formed to the area of the entire plane is 20 to 20%. It is preferably set to 70%.
  • the present invention can suitably produce a forged member as an automotive structural material having a thin portion having a thickness of 10 mm or less and having a fine crystal structure region of 95% or more in the thin portion.
  • Examples of automobile parts constituted by a forged member having such a shape include an upper arm in a wishbone structure front suspension and a toe control arm in a multi-link structure rear suspension.
  • the present invention is not limited to these automobile parts and the shapes shown in FIG. Further, the present invention is not limited to the above-described preferred range indicated by numerical values.
  • the aluminum alloy forged member of the invention [5] is lightweight and has excellent mechanical properties.
  • the mechanical characteristics can be further improved since the variation in the mechanical characteristics of each part is small.
  • the automobile structural material of the invention [8] is lightweight and has excellent mechanical properties.
  • FIG. 1 is a perspective view showing an example of a forged member that can be manufactured by the manufacturing method of the present invention.
  • FIG. 2 is a graph showing the crystal structure state of the forged member under the relationship between the forging material temperature and the equivalent strain.
  • FIG. 3 is a graph showing the relationship between the forging material temperature and the total content of Fe, Cr, and Mn in the examples of the present invention.
  • FIG. 4 is a graph showing the relationship between the processing rate and equivalent strain in forging.
  • FIG. 5 is a block diagram showing a procedure for manufacturing a forged member according to an embodiment of the present invention.
  • FIG. 6 is a perspective view showing a disk sample for confirming the alloy composition used in the embodiment of the present invention.
  • FIG. 7 is a graph showing the relationship between the center equivalent strain value (relative value) and the fine recrystallization region range in the forged member.
  • a forging material made of an Al—Mg—Si alloy is used.
  • the forge member (forged product) which can solve said subject is obtained by specifying the alloy composition of this forge raw material, and the raw material temperature of a forge raw material.
  • the forging material is 0.35 to 1.2% by mass of Mg, 0.2 to 1.3% by mass of Si, 0.5% by mass or less of Cu, and 0.15% by mass or more of Fe.
  • the alloy composition contains 0.15% by mass or more of Cr, 0.05% by mass or less of Mn, and the balance of Al and inevitable impurities.
  • Mg coexists with Si to form an Mg 2 Si-based precipitate and contribute to improving the strength of the forged member (final product). Therefore, Mg needs to be contained.
  • the Mg content must be adjusted to 0.35 to 1.2% by mass, preferably 0.8 to 1.2% by mass.
  • Si coexists with Mg to form a Mg 2 Si-based precipitate and contribute to improving the strength of the final product. Therefore, Si needs to be contained.
  • Si can further increase the strength of the final product after the aging treatment by adding an excessive amount exceeding the amount sufficient to produce Mg 2 Si-based precipitates.
  • Cu increases the supersaturation of apparent Mg 2 Si based precipitate, by increasing the Mg 2 Si based precipitate, in order to significantly accelerate the age hardening of a final product, preferably contained.
  • the Cu content must be adjusted to 0.5% by mass or less, preferably 0.3 to 0.5% by mass.
  • each part of the forged member is not a simple recrystallized structure, but a region of 50% or more (preferably all) for each part is in a fine recrystallized state. It is possible to sufficiently suppress variations in mechanical properties.
  • the behavior of recrystallization during forging is a non-recrystallized structure when the amount of equivalent strain described below is small, with the composition of the forging material and the material temperature being constant, and coarse recrystallization occurs as the amount of equivalent strain increases. A crystal structure is formed, and when the amount of considerable strain is further increased, a fine recrystallized structure is changed.
  • the unrecrystallized structure, the coarse recrystallized structure, and the fine recrystallized structure are as described in the above [Summary of the Invention] section, but in addition, they are as follows.
  • the non-recrystallized structure is a state that is not changed from the crystal structure at the time of casting.
  • the average crystal grain size is 50 to 300 ⁇ m.
  • the average particle diameter can be obtained by a section method from an image obtained by observing the crystal structure with a microscope by a conventional method, for example, the following procedure.
  • a microphotograph of the cross-sectional structure of the forged product is taken at a magnification of 100 times, and a straight line with “L1” and “L2” is drawn on the photo arbitrarily in the vertical and horizontal lengths, respectively.
  • the number of grain boundaries existing in the form of intersecting the straight lines of the lengths “L1” and “L2” is counted as “n1” and “n2”, respectively, and the average particle diameter is calculated by the following mathematical formula (1).
  • the average grain size of the crystal grains obtained from the microphotograph is obtained.
  • the average particle size can be obtained without depending on the lengths of “L1” and “L2”.
  • the state of the recrystallized structure of the forged member in the relationship between the equivalent strain amount and the forging heating temperature is the state shown in the graph of FIG.
  • the horizontal axis indicates the equivalent strain
  • the vertical axis indicates the forging heating temperature (forging material temperature).
  • black diamonds in the figure indicate an uncrystallized structure state
  • black circles indicate a coarse recrystallized structure state
  • black square marks indicate a fine recrystallized structure state.
  • the boundary between the coarse recrystallized structure region and the fine recrystallized structure region can be represented by a substantially straight line (boundary line E1), and the upper left region from the boundary line E1 is an amorphous structure region and / or It is a coarse recrystallized texture region, and the lower right region is a fine recrystallized texture region.
  • the recrystallization occurrence behavior during forging is controlled as follows, and the fine recrystallized structure region in the forged member is 50% or more, preferably 90%. It can adjust to the above.
  • the processing rate of each part is obtained, or the equivalent strain of each part is obtained directly, and from there, the range of the processing rate of the forged member as a whole with respect to the forging material Alternatively, the equivalent distortion range K (see FIG. 2) is obtained.
  • the equivalent distortion of each part can be obtained by simulation as will be described later.
  • the processing rate and the equivalent strain have a monotonically increasing correlation.
  • the forging material temperature is set to “Tc” within the range of “Ta” to “Tb”, the coarse recrystallized structure region in the forged member at the set temperature Tc,
  • the average ratio (ratio) to the crystal structure region is the ratio (Kb /%) between the coarse recrystallized structure region range Ka and the fine recrystallized structure region range Kb in the equivalent strain range K at the set temperature Tc.
  • Ka the forging material temperature can be set by calculating backward from the desired ratio (Kb / Ka).
  • a desired ratio corresponding to the desired mixed state in the entire range K of the equivalent strain or the entire range of the processing rate is just to set a forge raw material temperature so that it may become (Kb / Ka).
  • the strain value Kc is obtained, the equivalent strain value Kc at the boundary position is set as the target equivalent strain, and the forging material heating temperature is calculated by applying it to the linear equation of the boundary line E1, and the temperature is set as the forging material temperature during forging. Just do it.
  • Ka and Kb are corrected using a distribution function of equivalent strain values so that Kc becomes a predetermined value.
  • a distribution function f (equivalent strain value) of the equivalent strain value of the entire forged member is obtained, and f (equivalent strain value) is integrated from the minimum value to the Kc value as “Ka”, and f (equivalent strain) Kc value is determined so that Kb / Ka is equal to or greater than a desired value when “Kb” is obtained by integrating the value) from the Kc value to the maximum value.
  • Forging raw material heating temperature can be calculated
  • the distribution function of the equivalent strain of the entire forged member may be obtained by sampling an appropriate portion to obtain the equivalent strain value, and then obtaining the distribution function.
  • the values of the vertical axis and the horizontal axis of the graph of FIG. 2 can be applied as they are within a slight difference range where the amounts of Fe, Cr, and Mn are about 0.01% by mass, respectively.
  • mass% is increased, an upset product is created using the alloy, a cross-sectional macroscopic structure is observed, and a recrystallized state is observed to create a graph similar to FIG.
  • the above-mentioned setting concept can be applied using a graph.
  • a desired forged member is manufactured by controlling the generation behavior of recrystallization during forging.
  • Fe, Cr, and Mn as components (elements) that are greatly involved in the recrystallization generation behavior during forging.
  • Fe, Cr, and Mn are contained as inevitable impurities in the forging material made of an Al—Mg—Si alloy.
  • the total content (% by mass) of Fe, Cr, and Mn should be adjusted to 0.5% by mass or less, preferably 0.3 to 0.5% by mass. It is good to adjust.
  • Mn 0.05% by mass or less. Note that the content of Mn is 0%, that is, Mn may not be contained.
  • the content is preferably 0.5% by mass or less in order to sufficiently secure the region of the fine recrystallized structure.
  • Forging material temperature (° C.) ⁇ ⁇ 260 (° C.) ⁇ [total content of Fe, Cr, Mn (mass%)] + 440 (° C.)
  • Forging material temperature (° C.) ⁇ ⁇ 260 (° C.) ⁇ [total content of Fe, Cr, Mn (mass%)] + 440 (° C.)
  • the present invention is a method for manufacturing a forged member using a predetermined shape, composition, and forging material temperature condition in accordance with these design procedures.
  • the design procedure 1 includes the following steps S11 to S15, and is a procedure for determining an optimal composition and the like from the shape of the product (forged member).
  • Step S11 When each shape of the forged material to be used and the forged product (forged member) to be manufactured is given, the equivalent strain at each part is formed from the forged material shape to the forged product shape. Obtained by simulating the process.
  • An example of software used in this simulation is forging analysis software “DEFFORM”.
  • Step S12 The equivalent strain range including all the equivalent strains of each part, that is, the equivalent strain range in the entire forged member is obtained, and the range is set as the equivalent strain range in FIG.
  • the graph of FIG. 2 is used as information associating the forging material temperature prepared in advance with the range of the equivalent strain.
  • Step S13 A ratio of a desired fine recrystallization region range, for example, 50%, is set for the entire molded product (forged member) within the set equivalent strain range, and the equivalent strain (target equivalent strain) corresponding to the ratio is set in FIG.
  • the upper limit value of the forging heating temperature is obtained from the target equivalent strain based on the graph of FIG.
  • Step S14 When the upper limit of the forging heating temperature is determined, the upper limit of the total amount of (Fe, Cr, Mn) is obtained from the temperature using the graph of FIG.
  • the graph of FIG. 3 is a graph showing the relationship between the forging material temperature (forging heating temperature) and the total content of Fe, Cr, and Mn, and details thereof will be described later.
  • Step S15 The alloy composition and the forging material temperature condition are obtained by the above procedure.
  • the design procedure 2 includes the following steps S21 to S25, and is a procedure for determining an optimum shape from the composition.
  • Step S21 When a material to be used is given, the total amount of (Fe, Cr, Mn) is obtained from the composition of the material.
  • Step S22 The upper limit of the forging material temperature is obtained from the total amount of (Fe, Cr, Mn) using the graph of FIG.
  • Step S23 The obtained upper limit of the forging material temperature is set as the forging material temperature on the vertical axis of the graph of FIG.
  • the graph of FIG. 2 is used as information associating the forging material temperature prepared in advance with the range of the equivalent strain.
  • Step S24 Based on the graph of FIG. 2, at the set forging material temperature, a predetermined fine recrystallization region range as the entire molded product (forged member), for example, an equivalent strain range satisfying 50% is obtained, and the range is determined. Allowable equivalent strain range. Specifically, based on the graph of FIG. 2, the target equivalent strain corresponding to the set forging material temperature is obtained, and from the target equivalent strain value to the strain value small side, the large side (the strain axis lateral direction in the figure), The equivalent strain range (Ka, Kb) is determined so that Kb / Ka is, for example, 50% or more.
  • Step S25 The shape of the forged material and the forged product (forged member) is designed within the allowable equivalent strain range.
  • the design procedure 3 includes the following steps S16 to S19 in addition to the design procedure 1 (steps S11 to S15), and is obtained by adding a fine adjustment loop to the setting procedure 1.
  • Steps S11 to S15 As described in the design procedure 1 above.
  • Step S16 The recrystallized state of the product (forged member) manufactured using the alloy composition and forged material temperature conditions obtained in steps S11 to S15 is evaluated by observing the macrostructure.
  • Step S17 The relationship between the obtained recrystallization state and the forging load is evaluated, and a forging load that can secure a predetermined fine recrystallization region range (for example, 50%) is used for the forging process based on the evaluation result. If it is necessary to make the value larger than the maximum load capacity value of the forging machine (preferably 80% of the maximum load capacity value) (if fine adjustment is necessary), the process returns to step S14 and the total amount of Fe, Cr, Mn Review the ingredients so that there is less.
  • a predetermined fine recrystallization region range for example, 50%
  • Step S18 The relationship between the obtained recrystallization state and the forging load is evaluated, and a forging load that can secure a predetermined fine recrystallization region range (for example, 50%) is used for the forging process based on the evaluation result. If there is a margin for the maximum load capacity value of the forging machine (preferably 80% of the maximum load capacity value) (if fine adjustment is required), the process returns to step S13 and the forging temperature is lowered. Review material temperature.
  • a predetermined fine recrystallization region range for example, 50%
  • Step S19 If fine adjustment is not necessary in steps S17 and S18, the setting procedure is terminated.
  • the lower limit of the forging material temperature is determined by a load at the time of forging processing. For example, lowering the material temperature during forging increases the load during molding, but the material temperature when the load matches the maximum load capacity value of the forging machine (preferably 80% of the maximum load capacity value) is the lower limit temperature. can do. More preferably, “( ⁇ 260 (° C.) ⁇ [total content of Fe, Cr, Mn (% by mass)] + 440 (° C.)) ⁇ 60 ° C.” is set as the lower limit temperature of the material temperature.
  • the equivalent strain amount “ ⁇ ” can be obtained based on the following relational expression.
  • the forging material is heated in the heating furnace based on the time until the forging material heated to the target forging material temperature is taken out of the heating furnace and forged, and the temperature reduction rate calculated in the temperature reduction rate calculation process.
  • the temperature drop width from when it is taken out to forging is obtained (temperature drop width calculation process).
  • the forging material is put into the forging die, the forging material is preheated at a temperature obtained by adding the temperature reduction width calculated in the temperature reduction width calculation process to the actual forging material temperature ( Preheating treatment).
  • a forging die is heated by being provided with a heating device (heating treatment with the die). It is desirable to set the mold temperature as close to the target forging material temperature as possible. However, if the temperature is too high, the effect of the lubricant during forging will be impaired, so the specified temperature range of the lubricant used. It may be set according to the upper limit of.
  • the process (1) to (3) may be sequentially performed by omitting the process (4), or the processes (1), (2), and (4) may be performed by omitting the process (3). May be performed sequentially.
  • a casting process, a soaking process, a forging process (hot forging process), and a post-forging process are performed in this order, and forging is performed.
  • a member (forged product) is manufactured.
  • the casting process is a process for obtaining the forging material. That is, in this embodiment, the forging material which consists of said composition is obtained by a continuous casting method.
  • a continuous casting method such as a hot top vertical continuous casting method, a gas pressure type hot top vertical continuous casting method, a horizontal continuous casting method, or the like can be suitably used.
  • the casting speed is preferably as high as possible (for example, 200 to 1000 mm / min) within a range in which ingot breakage does not occur from the viewpoint of refinement of the ingot structure.
  • the soaking process soaking is performed on the cast rod as the forging material.
  • the cast rod obtained in the casting process has a coarse Fe—Cr—Mn precipitate in order to remove microsegregation and prevent the movement of grain boundaries during recrystallization and maintain a fine recrystallized structure.
  • a soaking process is performed for the purpose of achieving the above.
  • the soaking condition is to hold the cast bar at, for example, 570 to 550 ° C. for 4 to 10 hours.
  • forging processing
  • forging can be performed using a known forging apparatus (forging machine) under known forging conditions from the past, except for the conditions specific to the present application such as the material components and temperature conditions described above. .
  • the forging material is subjected to peripheral cutting and cutting processing to a predetermined length, if necessary, before being put into the die of the forging device. Further, the forging material and the forging die are subjected to a lubricant coating treatment as necessary.
  • solution treatment, quenching treatment, and aging treatment can be performed as necessary, for example, for the purpose of improving strength.
  • the solution treatment condition is that the forged member (forged product) is held at 525 to 570 ° C., for example, 560 ° C., and held for 0.5 to 3 hours, for example, 4 hours after the forged member reaches the target temperature.
  • the quenching treatment conditions are such that the forged member is hot-quenched at 60 ° C., for example. Under these quenching conditions, the temperature should be as low as possible (5 to 25 ° C.) to improve the characteristics, and as high as possible (40 to 70 ° C.) to prevent distortion.
  • the aging treatment condition is that the forged member is held at a temperature of 175 to 185 ° C. for 5.5 to 6.5 hours. For example, the forged member is held at 180 ° C. for 6 hours.
  • the forged member (forged product) obtained through these steps is in a recrystallized structure state depending on the amount of equivalent strain at each part, but at least 50% or more in the equivalent strain at each part.
  • the region is in a fine recrystallized state. Since the region of 50% or more is in the state of fine recrystallized structure, for each part, there is little variation in the mechanical properties, especially the tensile properties with respect to the difference in the plastic working rate, and the structural aluminum alloy forged member with excellent corrosion resistance become.
  • the forged member obtained by the present embodiment has a tensile strength value exceeding 250 MPa, which is considered preferable.
  • the reason is that if the fine recrystallization region in each part is 50% or more, the crystal grains in the coarse recrystallized region are also refined to some extent, so that the strength of the coarse recrystallized grain region is hardly reduced, and the member cross section This is because the mechanical strength as a whole is improved.
  • the forged aluminum alloy member produced according to the present embodiment is small and light, and has excellent mechanical properties and corrosion resistance. Therefore, it can be a high-strength and lightweight structural material excellent in corrosion resistance. Therefore, the aluminum alloy forged member obtained by the present invention is a structural material for automobiles, for example, an automobile underbody member, an automobile frame member, an automobile bumper member, an automobile steering member, a motorcycle frame member, and a motorcycle steering member. It can be suitably employed for bicycle frame members, bicycle steering members, bicycle crank members, and the like.
  • the forged member according to the present invention When the forged member according to the present invention is applied to a structural material for automobiles, it becomes possible to improve the motion performance and environmental performance of the vehicle on which the forged member is mounted.
  • a molten aluminum alloy to which a predetermined metal was added was used to continuously cast a round bar having a diameter of 55 mm using a hot top casting machine, and Al alloys of Examples 1 to 8 and Comparative Examples 1 to 10 were used. Continuous cast round bars corresponding to the composition were prepared. The casting speed was 400 mm / min.
  • each aluminum alloy melt is cast into a mold, a disk sample having a shape as shown in FIG. 6 is collected, and each component is analyzed by emission spectroscopic analysis in accordance with JIS H 1305. Each was analyzed, and the alloy composition of the disk sample corresponding to each continuously cast round bar was confirmed.
  • the round bar obtained by continuous casting was cut into a standard length and homogenized at 560 ° C. for 7 hours.
  • the outer periphery of the continuous cast round bar after the homogenization treatment was cut to a diameter of 50 mm and cut to a length of 60 mm to produce a round bar-like forging material.
  • the round bar-like forging material thus obtained was preheated at the forging material temperature shown in Table 1, and then forged using a conventional forging machine such as a knuckle joint press.
  • a conventional forging machine such as a knuckle joint press.
  • the equivalent strain at the center is 0 (no upset), 0.67, 1.33, 1.67, 2.00, 4.00.
  • the thickness after installation was changed.
  • These upset products were subjected to a solution treatment at 540 ° C. for 4 hours, followed by quenching in warm water at 60 ° C., and an aging treatment at 180 ° C. for 5 hours. Thereafter, the installed product was air-cooled to obtain forged members (samples) of Examples 1 to 8 and Comparative Examples 1 to 10.
  • the equivalent strain amount was calculated by simulating the same process as the upsetting process. At this time, the processing rates are 0, 25, 50, 75, 80, and 95%, respectively.
  • the processing rate is defined below.
  • [Processing rate] (Material height before installation-Material height after installation) / Material height before installation x 100
  • the JIS14A proportional test piece was extract
  • the tensile strength value within ⁇ 5% with respect to the tensile strength of the test piece having an equivalent strain of 0 was determined to have few variations in tensile strength as an effect of the present invention.
  • the reason for the determination is that it was considered that the variation in the tensile strength value within ⁇ 5% was caused by factors other than the factor of the present invention (fine recrystallization region).
  • Table 2 shows the results of these tensile tests.
  • the forging material temperature condition of the present invention that is, [forging temperature (° C.)] ⁇ ⁇ 260 ⁇ [total content of Fe, Cr, Mn (mass%)] + 440 Since this condition was not satisfied, coarse recrystallization occurred in all or part of the equivalent strain from 0.67 to 4.00, and variations in tensile strength occurred.
  • tissue state of each sample of Examples 1 to 8 and Comparative Examples 1 to 10 was observed as follows.
  • the cross section of the sample was mirror-finished with a milling cutter, the processed surface was etched with an aqueous sodium hydroxide solution, the corrosion products were removed with nitric acid, and then dried to reveal a macrostructure. The revealed macrostructure was visually observed to determine the tissue state.
  • the fine recrystallized structure state was 50% or more in all the center equivalent strains of 0.67 or more.
  • the fine recrystallization region was 65% within the observation range.
  • the coarse recrystallized region was 25%, and the other part was an unrecrystallized structure.
  • the fine recrystallization region is a structure region having an average particle size of (0.05 to 10) ⁇ “crystal average particle size during casting”, and the coarse recrystallization region is (10 ⁇ 100) ⁇ A structure region of “crystal average grain size at casting”.
  • the fine recrystallized structure region was 90%, and in the center equivalent strain of 1.67 or more, the fine recrystallized structure region was 100%.
  • the equivalent strain of 0 means that forging is not performed, and in an actual forged product, at least the processing rate is 25% or more (equivalent strain of 0.67 or more).
  • FIG. 7 is a graph showing the relationship between the range of the fine recrystallized structure region and the equivalent strain value in the forged member.
  • Example 1 when only the wrinkle equivalent strain is changed at the same composition and the same forging material temperature, the change in the fine recrystallization region range is monotonously increased.
  • the fine recrystallization region range can be 50% or more by setting the center equivalent strain of each part of the forged product to a predetermined value or more. As a result, variation in tensile strength can be reduced as a whole forged product.
  • Comparative Examples 1 and 2 since the composition is a JIS6061 alloy and the forging material temperature is high, the recrystallized grains become coarse, the tensile strength decreases as a result of the evaluation, and the tensile strength variation is larger than ⁇ 5%. It has become. Incidentally, Comparative Examples 1 and 2 differ from Example 1 only in the material temperature, and correspond to Example 1 when forging at a lower material temperature.
  • Comparative Examples 5 and 6 are high-strength materials having a composition of 6000 series, but because the forging material temperature is low, coarse recrystallization occurs, the tensile strength decreases as a result of the evaluation, and further, the tensile strength variation is ⁇ 5. It is larger than%.
  • FIG. 3 is a graph showing the relationship between the forging material temperature (° C.) indicated on the vertical axis (Py) and the total content (mass%) of Fe, Cr, and Mn indicated on the horizontal axis (Px).
  • examples are indicated by black rhombus marks, and comparative examples are indicated by black square marks.
  • the numbers attached to these marks are the numbers of the examples or comparative examples.
  • the black diamonds attached with the numbers “1” are the data of Example 1, and the numbers “3”.
  • the black square mark with “” is data of Comparative Example 3.
  • the continuously cast round bar was cut into a fixed length in the same manner as described above, and homogenized at 560 ° C. for 7 hours.
  • the outer periphery of the continuous cast round bar after the homogenization was cut to a diameter of 50 mm and cut to a length of 60 mm to produce a round bar-shaped forging material.
  • Examples 1 to 8 satisfied all the requirements of the present invention, and therefore had excellent tensile strength and excellent stress corrosion cracking property.
  • the equivalent strain In the range of 0.67 to 4 that is, in the range of the processing rate of 25 to 95, at least about 50% or more of each part has a fine recrystallized structure. It is possible to produce a forged product that is light in weight and excellent in mechanical properties and corrosion resistance.
  • Example based on design procedure 1> With respect to the shape shown in FIG. 1, the composition and forging material temperature conditions are determined and the forged member is manufactured based on the design procedure 1 described above, as shown in the following steps S11 to S15. Was 60%, and a forged member having sufficient mechanical properties and excellent corrosion resistance was obtained.
  • Step S11 From the forging material to be used and each shape in FIG. 1, the equivalent strain at each part was obtained by simulating the forming process from the forging material shape to the forged product shape (software used in the simulation) Wear is forging analysis software "DEFFORM"). The distribution of relative strain values was 0.7 to 2.0. The distribution of the equivalent strain value was processed as a uniform distribution because it is difficult to obtain the distribution in the actual product exactly.
  • Step S12 0.7-2.0 was set as the equivalent strain range in FIG.
  • Step S13 The ratio of the fine recrystallization region range is set to 60%, the equivalent strain corresponding to the ratio (target equivalent strain) is set to 1.15 from the graph of FIG. 2, and the upper limit of the forging material heating temperature based on the graph The value was 360 ° C.
  • Step S14 Since the upper limit value of the forging heating temperature is 360 ° C., the upper limit of the total amount of (Fe, Cr, Mn) is set to 0.37% from the temperature using the graph of FIG.
  • Step S15 By the above procedure, the upper limit of the total amount of the alloy composition (Fe, Cr, Mn) was set to 0.37%, and the forging material temperature condition upper limit was 360 ° C.
  • Step S21 It was decided to use a material having a total composition (Fe, Cr, Mn) of 0.37% or less.
  • Step S22 Using the graph of FIG. 3, the upper limit of the forging material temperature was set to 360 ° C. from the total amount of (Fe, Cr, Mn).
  • Step S23 The upper limit 360 ° C. of the obtained forging material temperature was set as the forging material temperature on the vertical axis of the graph of FIG.
  • Step S24 The ratio of the fine recrystallization region range is set to 60%, and based on the graph of FIG. 2, at the set forging temperature of 360 ° C., Kb / Ka is equivalent to 60% at the intersection with the formula E1.
  • Step S25 For the shape shown in FIG. 1 (but without the meat stealing part), from the forging material to be used and each shape in FIG. 1, the equivalent strain at each part is changed from the forging material shape to the forged product shape.
  • the equivalent strain range was 0.5 to 2.0. Since the lower limit is lower than the upper and lower limits obtained in step 24, the shape was changed to increase the lower limit of the equivalent strain value, and a meat stealing portion was provided. As a result, the equivalent strain lower limit value was 0.7, so the final shape was determined.
  • the method for manufacturing a forged member of the present invention can be applied to a forging technique using a forged material made of an aluminum alloy.
PCT/JP2011/059373 2010-04-16 2011-04-15 アルミニウム合金鍛造部材の製造方法 WO2011129431A1 (ja)

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CN102912199A (zh) * 2012-10-29 2013-02-06 虞海香 一种车身用铝合金薄板
CN104404350A (zh) * 2014-11-17 2015-03-11 柳州市俊杰汽配制造有限公司 一种汽车用控制臂
CN104455068A (zh) * 2014-11-17 2015-03-25 柳州市俊杰汽配制造有限公司 一种汽车用分离轴承
JP2015127064A (ja) * 2013-11-26 2015-07-09 昭和電工株式会社 ハードディスクドライブ装置ケースボディ用鍛造素形材、ケースボディ、ケースボディ用鍛造素形材の製造方法、およびケースボディの製造方法
WO2016129127A1 (ja) * 2015-02-10 2016-08-18 昭和電工株式会社 アルミニウム合金製塑性加工品、その製造方法及び自動車用部品
CN113486459A (zh) * 2021-06-22 2021-10-08 南京钢铁股份有限公司 基于deform模拟预防低合金结构钢折弯开裂的方法
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CN108913963A (zh) * 2018-06-22 2018-11-30 镇江市益宝电气科技有限公司 一种高强度耐腐蚀母线槽

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EP2425911A1 (en) * 2009-04-30 2012-03-07 Showa Denko K.K. Process for producing cast aluminum alloy member
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CN102912199A (zh) * 2012-10-29 2013-02-06 虞海香 一种车身用铝合金薄板
JP2015127064A (ja) * 2013-11-26 2015-07-09 昭和電工株式会社 ハードディスクドライブ装置ケースボディ用鍛造素形材、ケースボディ、ケースボディ用鍛造素形材の製造方法、およびケースボディの製造方法
CN104404350A (zh) * 2014-11-17 2015-03-11 柳州市俊杰汽配制造有限公司 一种汽车用控制臂
CN104455068A (zh) * 2014-11-17 2015-03-25 柳州市俊杰汽配制造有限公司 一种汽车用分离轴承
WO2016129127A1 (ja) * 2015-02-10 2016-08-18 昭和電工株式会社 アルミニウム合金製塑性加工品、その製造方法及び自動車用部品
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US11247262B2 (en) * 2017-08-09 2022-02-15 Kobe Steel, Ltd. Vehicle knuckle
CN113486459A (zh) * 2021-06-22 2021-10-08 南京钢铁股份有限公司 基于deform模拟预防低合金结构钢折弯开裂的方法

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