CN105525170A - Aluminium alloy forging and method for producing the same - Google Patents

Aluminium alloy forging and method for producing the same Download PDF

Info

Publication number
CN105525170A
CN105525170A CN201510523468.3A CN201510523468A CN105525170A CN 105525170 A CN105525170 A CN 105525170A CN 201510523468 A CN201510523468 A CN 201510523468A CN 105525170 A CN105525170 A CN 105525170A
Authority
CN
China
Prior art keywords
forging
quality
crystal grain
aluminum alloy
grain diameter
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
CN201510523468.3A
Other languages
Chinese (zh)
Other versions
CN105525170B (en
Inventor
田中敏行
上高原廉树
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Publication of CN105525170A publication Critical patent/CN105525170A/en
Application granted granted Critical
Publication of CN105525170B publication Critical patent/CN105525170B/en
Expired - Fee Related legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • C22C21/12—Alloys based on aluminium with copper 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/14—Alloys based on aluminium with copper as the next major constituent with silicon
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/16—Alloys based on aluminium with copper as the next major constituent with magnesium
    • 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
    • C22C21/12—Alloys based on aluminium with copper as the next major constituent
    • C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
    • 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
    • C22F1/057—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with copper as the next major constituent

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Forging (AREA)

Abstract

Disclosed is an aluminum alloy forging having excellent high-temperature properties (e.g., fatigue strength in a high-temperature environment). The aluminum alloy forging is formed by forging an aluminum alloy. The aluminum alloy contains Cu in a content of 3.0 to 8.0 mass percent, Mg in a content of 0.01 to 2.0 mass percent, Ag in a content of 0.05 to 1.0 mass percent, and Mn in a content of 0.05 to 1.5 mass percent, with the remainder being Al and inevitable impurities. The aluminum forging has an average grain size of 500 [mu]m or less and a grain aspect ratio (length-to-width ratio) of 10 or less.

Description

Aluminum alloy forged material and manufacture method thereof
Technical field
The present invention relates to high-speed motion component aluminum alloy forged material and the manufacture method thereof carrying out at high speeds rotating or sliding.
Background technology
Aluminium has low density and the characteristic that high strength, handling ease are such.These characteristics are applied flexibly, in light weight and the Transport Machinery such as the rail truck of desired strength, processing characteristics, automobile, boats and ships, various mechanical component, engine component etc. in use aluminum alloy forged material.Specifically, such as rotate at high speeds at the piston etc. of the rotor such as generator, compressor (small-sized blade), rotary blade (large-scale blade), engine or use aluminum alloy forged material in the high-speed motion component that slides.
For the high-speed motion component for these purposes, being greater than the applied at elevated temperature environment of 100 DEG C, the properties of such component that carries out rotating and/or slide requires hot properties (thermotolerance and high-temperature yield strength).With in order to respond this requirement and the relevant disclosure of the invention of the aluminium alloy developed, aluminum alloy forged material in such as patent documentation 1 ~ 6.
Patent Document 1 discloses a kind of manufacture method of aluminum alloy forged material of hot properties excellence, it is characterized in that, it is containing Cu:4.0 ~ 7.0 quality %, Mg:0.2 ~ 0.4 quality %, the manufacture method of the aluminum alloy forged material that Ag:0.05 ~ 0.7 quality % and surplus are made up of aluminium and inevitable impurity, it has following characteristic: form the casting material that forms after the temperature of 500 ~ 545 DEG C carries out homogenizing thermal treatment by by this, forge hot is carried out the temperature of 280 ~ 360 DEG C, solution and quench treatment is carried out afterwards the temperature of 510 ~ 545 DEG C, after implementing artificial age-hardening's process, aluminum alloy forged material is now more than 400MPa in the yield strength of room temperature.
Patent Document 2 discloses a kind of aluminum alloy forged material of high temperature fatigue strength excellence, it is characterized in that, it is containing Cu:4.0 ~ 7.0 quality %, Mg:0.2 ~ 0.4 quality %, Ag:0.05 ~ 0.7 quality %, V:0.05 ~ 0.15 quality % and surplus by aluminium and the inevitable aluminum alloy forged material that forms of impurity, the distribution density of the Al-V system precipitate in forging material tissue is 1.5/(μm) 3above.
Patent Document 3 discloses a kind of high-speed motion component aluminium alloy cold forging material, it is characterized in that, it comprises Cu:1.5 ~ 7.0 quality %, the aluminium alloy cold forging material that Mg:0.01 ~ 2.0 quality % and surplus are made up of aluminium and inevitable impurity, its by microtexture have θ ' mutually and/or Ω phase and crystal grain diameter be less than 500 μm etc. axle recrystal grain form, in the tissue of these axle recrystal grains with the area occupation ratio of the fine recrystal grain of less than 1 μm of the form aggregate be mutually close to for less than 10%, 1000 hours creep rupture strengths are 250N/mm 2above and high-temperature yield strength is 280N/mm 2above.
Patent Document 4 discloses a kind of extension processing heat-resisting aluminium alloy of tenacity excellent, it is characterized in that, containing Cu5.1 ~ 6.5% (mass%, down together), Mg0.10 ~ 0.7%, Ag0.10 ~ 1.0%, Mn0.10 ~ 0.50%, Ti0.22 ~ 0.50%, and Mn amount is positioned at the scope of 0.5 ~ 2.5 with the ratio Mn/Ti of Ti amount, surplus is made up of Al and inevitable impurity.
Patent Document 5 discloses a kind of aluminum alloy forged material of excellent heat resistance, it is characterized in that, containing Cu5.1 ~ 6.5% (mass%, lower with), Mg0.30 ~ 0.70%, Ag0.10 ~ 1.0%, Mn0.10 ~ 0.50%, Cr0.07 ~ 0.11%, Ti0.06 ~ 0.30% and surplus by Al and inevitably the aluminium alloy that forms of impurity 200 DEG C, Creep Rupture Lifetimes under 160MPa is more than 500 hours.
Patent Document 6 discloses a kind of aluminium alloy of hot properties excellence, it is characterized in that, containing Si: be greater than 0.1 quality % and below 1.0 quality %, more than Cu:3.0 quality % and below 7.0 quality %, more than Mn:0.05 quality % and below 1.5 quality %, more than Mg:0.01 quality % and below 2.0 quality %, more than Ti:0.01 quality % and below 0.10 quality %, more than Ag:0.05 quality % and below 1.0 quality %, and Zr is limited in and is less than 0.1 quality %, surplus is made up of Al and inevitable impurity.
Prior art document
Patent documentation
Patent documentation 1: Japanese Patent No. 4088546 publication
Patent documentation 2: Japanese Patent No. 4058398 publication
Patent documentation 3: Japanese Patent No. 3997009 publication
Patent documentation 4: Japanese Patent No. 4676906 publication
Patent documentation 5: Japanese Unexamined Patent Publication 2013-142168 publication
Patent documentation 6: Japanese Unexamined Patent Publication 2013-14835 publication
Summary of the invention
The problem that invention will solve
In recent years, for rotor, rotary blade etc., stability in high temperature environments, the improved performance of material behavior improve.Although invention is responded above-mentioned requirements and obtains disclosed in above-mentioned patent documentation 1,3 ~ 6, not yet any research is carried out for the fatigue strength improved in high temperature environments.Therefore, there is the such problem of the aluminum alloy forged material that cannot realize fatigue strength is in high temperature environments improved in invention disclosed in patent documentation 1,3 ~ 6.
Inventing disclosed in patent documentation 2 with V is neccessary composition, by making the so special precipitate of Al-V system precipitate separate out with specific distribution density, makes fatigue strength in high temperature environments improve thus.But, require the fatigue strength improved further in high temperature environments.
The present invention completes in view of such situation, the aluminum alloy forged material that problem is to provide hot properties (fatigue strength in high temperature environments) excellent and manufacture method thereof.
For the means of dealing with problems
The feature solving the of the present invention aluminum alloy forged material of above-mentioned problem is, it is the aluminum alloy forged material that will undertaken forging by Al and aluminium alloy that inevitably impurity is formed containing Cu:3.0 ~ 8.0 quality %, Mg:0.01 ~ 2.0 quality %, Ag:0.05 ~ 1.0 quality %, Mn:0.05 ~ 1.5 quality % and surplus and be formed, its average crystal grain diameter is less than 500 μm, and crystal grain diameter ratio (major axis/minor axis) is less than 10.
In aluminum alloy forged material of the present invention, above-mentioned aluminium alloy can containing one or more the element be selected from Zn:0.01 ~ 0.40 quality %, Si:0.01 ~ 1.00 quality %, V:0.01 ~ 0.15 quality %, Cr:0.01 ~ 0.30 quality %, Zr:0.01 ~ 0.50 quality %, Sc:0.01 ~ 1.00 quality % and Ti:0.01 ~ 0.20 quality %.
In addition, the feature solving the manufacture method of the of the present invention aluminum alloy forged material of above-mentioned problem is, it comprises: casting process, melts by the above-mentioned aluminium alloy formed that forms and is cast as casting material; Homogenize heat treatment step, to homogenize thermal treatment to above-mentioned casting material the maintenance temperature of 500 ~ 545 DEG C; Hot forging process, carries out to having carried out the above-mentioned heat treated casting material that homogenizes the forge hot that forging ratio is more than 1.5 the forging temperatures of 180 ~ 360 DEG C; Solution treatment operation, carries out solution treatment the maintenance temperature of 510 ~ 545 DEG C to the forging material carrying out above-mentioned forge hot; Quench treatment operation, is more than 10 DEG C/min with the average cooling rate between 400 ~ 290 DEG C and the condition being less than 30000 DEG C/min carries out quench treatment to the forging material carrying out above-mentioned solution treatment; And artificial age-hardening's treatment process, artificial age-hardening's process is carried out to the forging material carrying out above-mentioned quench treatment.
In the manufacture method of aluminum alloy forged material of the present invention, preferred above-mentioned forge hot is forged two different faces of above-mentioned casting material at least successively.
In the manufacture method of aluminum alloy forged material of the present invention, preferred above-mentioned forge hot is forged three different faces of above-mentioned casting material successively.
In the manufacture method of aluminum alloy forged material of the present invention, preferably above-mentioned forging temperature be set to more than 180 DEG C and be less than 280 DEG C.
The die forging temperature that the manufacture method of aluminum alloy forged material of the present invention can be included in 180 ~ 360 DEG C between above-mentioned hot forging process and above-mentioned solution treatment operation carries out the die forging operation of die forging to above-mentioned forging material.
In the manufacture method of aluminum alloy forged material of the present invention, preferably above-mentioned die forging temperature be set to more than 180 DEG C and be less than 280 DEG C.
Invention effect
The hot properties (fatigue strength in high temperature environments) of aluminum alloy forged material of the present invention is excellent.
The manufacture method of aluminum alloy forged material of the present invention can manufacture the excellent aluminum alloy forged material of hot properties (fatigue strength in high temperature environments).
Accompanying drawing explanation
Fig. 1 is the schema that the content of the manufacture method of aluminum alloy forged material to an embodiment of the invention is described.
Fig. 2 is the explanatory view be described method when calculating average crystal grain diameter and crystal grain diameter ratio (major axis/minor axis).
Fig. 3 is the explanatory view be described method when calculating average crystal grain diameter and crystal grain diameter ratio (major axis/minor axis).
Embodiment
Below, suitably with reference to accompanying drawing, the mode (embodiment) for implementing aluminum alloy forged material of the present invention and manufacture method thereof is described in detail.
[aluminum alloy forged material]
The aluminum alloy forged material of an embodiment of the invention (forging material hereinafter referred to as Al) is undertaken forging being formed by containing Cu:3.0 ~ 8.0 quality %, Mg:0.01 ~ 2.0 quality %, Ag:0.05 ~ 1.0 quality %, Mn:0.05 ~ 1.5 quality % and the aluminium alloy that surplus is made up of Al and inevitable impurity.The average crystal grain diameter of the Al forging material of present embodiment is less than 500 μm, crystal grain diameter ratio (major axis/minor axis) is less than 10.
This Al forges material to be equivalent to carry out Al forging material (see Fig. 1) of solution treatment operation S5 to artificial age-hardening treatment process S8 after hot forging process S3 described later terminates and to carry out die forging operation S4 after hot forging process S3 terminates, and the Al having carried out solution treatment operation S5 to artificial age-hardening treatment process S8 subsequently forges material (see also Fig. 1).In either case, (processing) the operation S7 that colds pressing all can carry out alternatively, and this has description below.Although the average crystal grain diameter of Al forging material of the present invention and crystal grain diameter ratio are also by the impact of composition, but substantially depend on the state of strain of the material internal be endowed under the forging condition of hot forging process S3 and/or die forging operation S4, by carrying out solution treatment operation S5, present with form, the i.e. average crystal grain diameter of tissue and crystal grain diameter ratio thus.The average crystal grain diameter presented by solution treatment operation S5 and crystal grain diameter can not be changed with process afterwards than substantially, in addition, are not also substantially changed than the effect obtained by presented average crystal grain diameter and crystal grain diameter.Therefore, for the calculating of average crystal grain and crystal grain diameter ratio, even if carry out quench treatment operation S6, artificial age-hardening treatment process S8 after solution treatment operation S5, also can measure.
It should be noted that, the Al of present embodiment forges in material, and aluminium alloy can containing one or more the element be selected from Zn:0.01 ~ 0.40 quality %, Si:0.01 ~ 1.00 quality %, V:0.01 ~ 0.15 quality %, Cr:0.01 ~ 0.30 quality %, Zr:0.01 ~ 0.50 quality %, Sc:0.01 ~ 1.00 quality % and Ti:0.01 ~ 0.20 quality %.
Below, the proterties of alloy composition and crystal grain is described respectively.
< alloying constituent > (Cu)
Cu is the basic ingredient of the Al forging material of present embodiment.Cu can by the effect of solution strengthening and precipitation strength both sides, and mainly makes Al forge the creep properties of material under normal temperature environment, creep properties in high temperature environments and high-temperature yield strength (fatigue strength in high temperature environments) to improve.More specifically, Cu makes θ ' phase, Ω phase in (100) face of Al alloy when the artificial age-hardening of high temperature processes, (111) face is fine and separate out to high-density, and the intensity that the Al after artificial age-hardening is processed forges material improves.This effect the content of Cu be more than 3.0 quality %, be more preferably more than 4.0 quality % time played.When the content of Cu is less than 3.0 quality %, above-mentioned effect is little, and Al forges material cannot obtain sufficient creep properties and high-temperature yield strength under normal temperature environment He under hot environment.On the other hand, if the content of Cu is greater than 8.0 quality %, then intensity becomes too high, and the forging that Al forges material declines.
Therefore, the content of Cu is 3.0 ~ 8.0 quality %, is preferably 4.0 ~ 7.0 quality %, is more preferably 4.5 ~ 7.0 quality %.
It should be noted that, in this specification sheets, normal temperature refers to room temperature, particularly refers to the degree of about 25 DEG C, and high temperature refers to the temperature of more than about 100 DEG C.
(Mg)
Mg and Cu is same, can by the effect of solution strengthening and precipitation strength both sides, and mainly makes Al forge material creep properties in high temperature environments, normal temperature yield strength and high-temperature yield strength to improve.More specifically, Mg and Cu is same, make when the artificial age-hardening of high temperature processes θ ' phase, Ω phase in (100) face of Al alloy, (111) face is fine and separate out to high-density, the intensity that the Al after artificial age-hardening is processed forges material improves.This effect is played when the content of Mg is more than 0.01 quality %.When the content of Mg is less than 0.01 quality %, above-mentioned effect is little, and Al forges material cannot obtain sufficient creep properties, normal temperature yield strength and high-temperature yield strength in high temperature environments.On the other hand, if the content of Mg is greater than 2.0 quality %, then intensity becomes too high, and the forging that Al forges material declines.
Therefore, the content of Mg is 0.01 ~ 2.0 quality %, is preferably 0.01 ~ 1.5 quality %, is more preferably 0.01 ~ 1.0 quality %.
(Ag)
Ag forges in material at Al and formation can be made fine and uniform Ω phase and there is not the region (PFZ of precipitated phase; Solute-depleted precipitate free zone) width is very narrow.Therefore, Ag can make the normal temperature strength of Al forging material, hot strength and High-Temperature Creep Performance improve.When the content of Ag is less than 0.05 quality %, this effect is little.On the other hand, even if the content of Ag is greater than 1.0 quality %, its effect is also saturated.
Therefore, the content of Ag is 0.05 ~ 1.0 quality %, is preferably 0.05 ~ 0.7 quality %.
(Mn)
Mn makes Al forge the microtexture generation fibrous tissue of material, thus normal temperature strength and hot strength are improved.Further, Mn makes when homogenizing thermal treatment to separate out in Al alloy substrate as the Al-Mn system dispersed particle of heat-staple compound.As this dispersed particle, Al can be enumerated 20cu 2mn 3.This dispersed particle has the effect of the crystal boundary movement after hindering recrystallize, therefore effective to preventing coarse grainsization.When the content of Mn is less than 0.05 quality %, makes the effect of normal temperature strength and hot strength raising, prevent the effect of coarse grains little.On the other hand, if the content of Mn is greater than 1.5 quality %, then easily generate thick infusibility intermetallic compound when melting casting, become Al and forge the cob webbing of material and the reason of destruction.
Therefore, the content of Mn is 0.05 ~ 1.5 quality %, is preferably 0.05 ~ 1.0 quality %, is more preferably 0.05 ~ 0.8 quality %.
(surplus)
Surplus is Al and inevitable impurity.As inevitable impurity, such as, Ni, Fe etc. can be enumerated.For inevitable impurity, as long as these elements add up to, about 0.15 quality % is following does not just affect effect of the present invention, and therefore the content of this degree can allow.
(Zn)
Zn, owing to forming the miniaturization compound of Mg-Zn system, thus can make intensity improve.The content of Zn does not have unusual effect when being less than 0.01 quality %.On the other hand, if the content of Zn is greater than 0.40 quality %, then corrosion proof decline is produced.
Therefore, the content of Zn is preferably 0.01 ~ 0.40 quality %, is more preferably 0.10 ~ 0.30 quality %.
(Si)
Si is improved the effect that Al forges the intensity of material.By adding Si, be tending towards increasing to the effective precipitate of raising intensity.In addition, by adding Si, effective to the dislocation loop suppressed in Al alloy.Therefore, the interpolation of Si to the miniaturization of precipitated phase, evenly precipitation effectively.When the content of Si is less than 0.01 quality %, these effects are little.On the other hand, if the content of Si is greater than 1.0 quality %, then produce thick intermetallic compound, cob webbing when becoming the die forging carrying out the high speed moving members such as rotor, rotary blade, piston, the decline of Fatigue Strength of Metal, the reason of destruction.
Therefore, the content of Si is preferably 0.01 ~ 1.00 quality %, is more preferably 0.01 ~ 0.60 quality %.
(V)
V can separate out in Al alloy substrate with the form of Al-V based compound, thus fatigue strength is in high temperature environments improved.In addition, V also makes when homogenizing thermal treatment to separate out the Al-V system dispersed particle as heat-staple compound in Al alloy substrate.This dispersed particle has the effect of the crystal boundary movement after hindering crystallization, therefore effective to preventing coarse grainsization.
By this effect, V can make Al forge the microtexture generation fibrous tissue of material, thus improves normal temperature strength and hot strength, fatigue strength especially in high temperature environments.Further, the effect that stable phase is separated out thickly is little compared with Zr, Cr, Mn, therefore makes normal temperature strength, hot strength and fatigue strength in high temperature environments improve, thus more preferably.
Thus, make below crystal grain diameter miniaturization to 500 μm for ensureing to guarantee Al to forge the object of the hot properties of material more reliably, therefore the content of V is preferably optionally containing reaching 0.01 ~ 0.15 quality %.When the content of V is less than 0.01 quality %, these effects are little.On the other hand, if the content of V is greater than 0.15 quality %, then easily generate thick infusibility intermetallic compound when melting casting, become Al and forge the cob webbing of material and the reason of destruction.
Therefore, the content of V is preferably 0.01 ~ 0.15 quality %, is more preferably 0.01 ~ 0.10 quality %.
(Cr)
Cr and V is same, when homogenizing thermal treatment, forging in the tissue of material the Al-Cr system dispersed particle as heat-staple compound is separated out at Al.This dispersed particle has the effect of the crystal boundary movement after hindering recrystallize, and to preventing, the coarsening of crystal grain is effective.When the content of Cr is less than 0.01 quality %, prevent the effect of the coarsening of crystal grain little.On the other hand, if the content of Cr is greater than 0.30 quality %, then easily generating thick infusibility intermetallic compound when melting casting, becoming Al and forging the cob webbing of material and the reason of destruction.
Therefore, the content of Cr is preferably 0.01 ~ 0.30 quality %, is more preferably 0.01 ~ 0.15 quality %.
(Zr)(Sc)
Zr and Sc, when homogenizing thermal treatment, makes to forge at Al respectively in the tissue of material as the Al-Zr system dispersed particle of heat-staple compound and Al-Sc system dispersed particle to separate out.These dispersed particles have the effect of the crystal boundary movement after hindering recrystallize, therefore effective to preventing the coarsening of crystal grain.If the content that the content of Zr is less than 0.01 quality % or Sc is less than 0.01 quality %, then prevent the effect of the coarsening of crystal grain little.On the other hand, if the content that the content of Zr is greater than 0.50 quality % or Sc is greater than 1.00 quality %, then easily generating thick infusibility intermetallic compound when melting casting, becoming the cacoplastic reason that Al forges material.
Therefore, when containing Zr and Sc, the content of Zr is preferably 0.01 ~ 0.50 quality %, and the content of Sc is preferably 0.01 ~ 1.00 quality %.
(Ti)
Ti has the effect of crystal grain miniaturization when making casting.When the content of Ti is less than 0.01 quality %, this effect is little.On the other hand, if when the content of Ti is greater than 0.20 quality %, form thick intermetallic compound.Further, this intermetallic compound becomes the starting point that Al forges the destruction of material when formed machining, is greater than 0.20 quality % if therefore add, then Al forges the plasticity decline of material.
Therefore, the content of Ti is 0.01 ~ 0.20 quality %.
(Fe)
Fe is mixed into usually used as inevitable impurity.But it is the element be mixed into from waste material etc., also have and improve the effect that Al forges the hot properties of material, thus content can to 0.15 quality %.If the content of Fe is greater than 0.15 quality %, then generates infusibility intermetallic compound, easily become the reason of cob webbing and destruction.
(average crystal grain diameter and crystal grain diameter ratio (major axis/minor axis))
Although Al of the present invention forges average crystal grain diameter and the impact being also subject to composition described above of crystal grain diameter ratio of material, but substantially depending on the state of strain of the material internal given under the forging condition of hot forging process S3, die forging operation S4, presenting with the form of tissue by carrying out solution treatment operation S5.That is, average crystal grain diameter and crystal grain diameter ratio can by carrying out hot forging process S3 and/or die forging operation S4 controls under forging condition described later.
Average crystal grain diameter can calculate as follows.First, as shown in Figure 2, cut the sample of measurement site with the size of about 15mm × 15mm × 10 ~ 20mm from product or test material, imbed resin.Further, carry out electrolytically etching after the face imbedding the sample after resin is ground, carry out photograph taking by opticmicroscope.Multiplying power during photograph taking correspondingly can adjust arbitrarily with the size of crystal grain diameter.
The mensuration of crystal grain diameter can be undertaken by so-called section method.That is, the measurement example of crystal grain diameter, as shown in Figure 3, respectively marks 3 lines (a1 ~ a3 of Fig. 3, b1 ~ b3) respectively equably at the vertical and horizontal of optical microscope photograph, measures the quantity of the crystal boundary that every root passes through.Crystal grain diameter calculates according to the quantity of the multiplying power of photo, size and crystal boundary.A series of mensuration is carried out with three photos, according to the mensuration of vertical 9 (namely 3 × 3), horizontal 9 (namely 3 × 3), obtain the crystal grain diameter of N=9 respectively in length and breadth, calculate the average of crystal grain diameter respectively according to longitudinal and transverse, obtain longitudinal and transverse respective average crystal grain diameter.Further, in the present invention, further longitudinal and transverse respective average crystal grain diameter is added and after calculate that it is average, thus as average crystal grain diameter.
In addition, crystal grain diameter ratio (major axis/minor axis) can obtain as follows: the mean value using longitudinal and transverse respective crystal grain diameter, using larger crystal grain diameter as major axis, less of minor axis, calculates crystal grain diameter ratio.
Present inventor has performed various research, found that, be less than 500 μm and make crystal grain diameter ratio (major axis/minor axis) be less than 10 by making average crystal grain diameter, fatigue strength in high temperature environments improves thus.If average crystal grain diameter is greater than 500 μm, then not only easily produce the incipient crack becoming the reason of fatigure failure, and the progress of crackle also accelerates, and can not realize the fatigue strength improved in high temperature environments.In addition, if crystal grain diameter ratio (major axis/minor axis) is greater than 10, then the orientation of crystallization is affected, and the anisotropy of the material behaviors such as fatigue strength in high temperature environments, creep properties, the strength of materials becomes large, can not manufacture the product of homogeneous.According to these research, average crystal grain diameter is set to less than 500 μm and crystal grain diameter ratio (major axis/minor axis) is set to less than 10.Crystal grain diameter is than being preferably less than 7, being more preferably less than 5.
Be less than 500 μm by making average crystal grain diameter and make crystal grain diameter ratio (major axis/minor axis) be less than 10; in duplex grain structure, appreciable particle diameter is not the group after the fine-grain aggregate of less than 1 μm, the thick recrystal grain counting mm ~ number about cm or residual ingot structure thus; fatigue strength is in high temperature environments good, can have the hot propertiess such as creep properties and machinability concurrently.It should be noted that, the Al preferred grain structure forged in material not necessarily refers to 100% tissue being only the crystal grain of above-mentioned certain size, as long as the scope that the hot propertiess such as fatigue strength in high temperature environments, machinability, creep properties can not be made to decline, just allows to be mixed into cast structure, duplex grain structure.
Such as, disperse existence respectively even if the fine-grain that particle diameter is less than 1 μm is single crystal grain, the hot properties such as fatigue strength, creep properties in high temperature environments also can not be made to decline.But, when it is with the form grouping of the world economy be mutually close to and even aggregate, machinability, hot properties can be made to decline.Therefore, by this point, in the microtexture after preferred solution treatment, the area occupation ratio of the fine-grain of less than 1 μm of aggregate is less than 10%.
In addition, even if such as crystal grain diameter disperses respectively than the crystal grain being greater than 10, the hot properties such as fatigue strength, creep properties in high temperature environments also can not be made to decline.But, when it is with the form grouping of the world economy be mutually close to and even aggregate, machinability, hot properties can be made to decline.Therefore, by this point, in the microtexture after preferred solution treatment, the crystal grain diameter of aggregate is less than 10% than the area occupation ratio of the crystal grain being greater than 10.
[manufacture method of aluminum alloy forged material]
Then, with reference to Fig. 1, the manufacture method of the Al of an embodiment of the invention being forged to material is described.
As shown in Figure 1, the manufacture method of the Al forging material of present embodiment comprises casting process S1, the heat treatment step S2 that homogenizes, hot forging process S3, solution treatment operation S5, quench treatment operation S6 and artificial age-hardening treatment process S8, by carrying out these operations successively, above-mentioned Al can be manufactured and forge material.
It should be noted that, in this manufacture method, die forging operation S4 can be comprised as required between hot forging process S3 and solution treatment operation S5.As mentioned above, the forging material after carrying out die forging operation S4 is also that Al of the present invention forges material.
In addition, (processing) the operation S7 that colds pressing can be comprised as required after quench treatment operation S6.
In addition, T6 described later is modified, T61 is modified can utilize solution treatment operation S5, quench treatment operation S6 and artificial age-hardening treatment process S8 to carry out.
In addition, T652 modifiedly can utilize solution treatment operation S5, quench treatment operation S6, (processing) the operation S7 and artificial age-hardening treatment process S8 that colds pressing carries out.It should be noted that, these are modified suitably can select according to the size of manufactured component, purposes.
It should be noted that, in this specification sheets, as modified concrete example, enumerate that T6 is modified, T61 is modified and T652 is modified is described, but be not limited thereto, even the forging material after to carry out beyond these modified is also included within the present invention.
(casting process)
The Al alloy with above-mentioned composition melts and is cast as the operation of casting material by casting process S1.Castmethod is not particularly limited, and uses known method.Such as, can by the castmethod suitably selected from common melting casting such as continuous casting rolling, semicontinuous casting method (DC casting) etc., use melts the Al alloy molten solution be adjusted in composition range of the present invention and is cast as ingot casting.
(homogenize heat treatment step)
The heat treatment step S2 that homogenizes preferably at high temperature to carry out in the temperature range that eutectic melting do not occur as much as possible the maintenance temperature of 500 ~ 545 DEG C.In addition, for the heat treated time that homogenizes, according to the time etc. being suitable for composition, cast ingot dimension, manufacture, suitably can set the time of intermetallic compound to the melting in mother metal, diffusion effectively can be carried out.Heat treated time that homogenizes such as preferably carries out 8 ~ 100 hours.By such condition, effectively carry out intermetallic compound thus to the melting in mother metal, diffusion.Its result, can reduce the size of intermetallic compound.It should be noted that, the multistage heat treating method that the homogenizes thermal treatment that homogenizes being divided at least two benches to carry out according to the kind of intermetallic compound is as being used for reducing the method for intermetallic compound under the condition that eutectic melting does not occur and more effective.
This multistage heat treating method that homogenizes sets suitable condition (heat-up rate, homogenization temperature, treatment time) accordingly by the kind with intermetallic compound to carry out.Such as, as the appropriate heat treatment to each intermetallic compound, by heat-treating under the comparatively low temperature of (500 ~ 545 DEG C) in heat treated temperature range that homogenizes, intermetallic compound fully being melted, spreading.Then, by reducing intermetallic compound homogenizing to heat-treat under the higher temperatures in heat treated temperature range.The thermal treatment that homogenizes adjusting temperature in the multistage is like this effective.
In addition, as the method that can obtain the same effect of homogenize heat treating method multistage with this, have and make the homogenize speed of thermal treatment temp of arrival be compared with low speed and the method for carrying out in the temperature range of eutectic melting heating up does not occur at intermetallic compound.The method also can combine with the above-mentioned multistage thermal treatment that homogenizes carries out.It should be noted that, heat-up rate now needs suitably to set according to the kind, size, amount etc. of intermetallic compound.
These heat treating methods that homogenize can prevent the eutectic melting of intermetallic compound and reduce the size of intermetallic compound.Because intermetallic compound diminishes, be that the fatigure failure of starting point is suppressed with intermetallic compound, fatigue strength in high temperature environments improves.In addition, by the thermal treatment that homogenizes, each element contained in intermetallic compound evenly spreads in mother metal, can be improved the intensity of mother metal thus by solution strengthening and precipitation strength.Meanwhile, the elongation of Al alloy, impact value and fatigue strength in high temperature environments can also be made further to improve.
In addition, by carrying out homogenizing thermal treatment, carry out the homogenizing of the microsegregation produced because solidifying, the precipitation of super saturated solid solution element, the conversion of the steady equilibrium phase in opposite directions that is situated between thus.When the heat treated temperature that homogenizes is less than 500 DEG C, the intermetallic compound not solid solutions such as the crystallisate of ingot casting, homogenize and become insufficient.On the other hand, if the heat treated temperature that homogenizes is greater than 545 DEG C, then the possibility that burning occurs improves.Therefore, the heat treated temperature that homogenizes is the scope of 500 ~ 545 DEG C.
Under carrying out the multistage heat treated situation that homogenizes, need to set heat-treat condition accordingly with the kind of intermetallic compound as described above.In addition, carry out, with in the heat treated situation that homogenizes heated up compared with lower velocity, needing too to set heat-treat condition accordingly with the kind of intermetallic compound.
(hot forging process)
Hot forging process S3 carries out to the heat treated casting material that carried out homogenizing the operation that forging ratio is the forge hot of more than 1.5 the forging temperature of 180 ~ 360 DEG C.By the forging condition (the forging direction etc. of forging temperature, Forging Equipment Speed, material) of this hot forging process S3 and die forging operation S4 described later, give strain to material internal.The crystal grain diameter obtained in the solution treatment operation S5 of subsequent processing, crystal grain diameter are than the intensity (direction, density etc.) substantially depending on this strain.It should be noted that, in these forging process, crystal grain diameter is only that the crystal grain of casting material there occurs distortion, the crystal grain diameter confirmed at this moment is not almost reflected in final crystal grain diameter (but, if the crystal grain diameter in casting material is little, then the crystal grain diameter after solution treatment operation is also tending towards little.)。If be placed in hot environment in solution treatment operation S5 described later under, then the strain of the material internal be imported in material in these forging process is released, form new crystal grain.
In order to realize improving characteristic, the fatigue strength especially in high temperature environments of Al alloy, the temperature condition of forge hot and forging ratio described later are all important.That is, the temperature condition of forge hot is important for the crystal grain diameter after the solution treatment operation S5 of control Al alloy, grain shape.Be 180 ~ 360 DEG C by forging temperature when making forge hot, the shape of crystal grain diameter and crystal grain can be controlled, and stably can manufacture Al and forge material.When the forging temperature of forge hot is less than 180 DEG C, when forge hot, Al alloy easily produces and breaks, and forging processing itself is difficult.On the other hand, if the forging temperature of forge hot is greater than 360 DEG C, then easily produce coarse grain in the tissue of Al alloy.Therefore, the hot properties that Al forges material declines, and the Al that can not manufacture hot properties excellence forges material.Therefore, forging temperature during forge hot is set to 180 ~ 360 DEG C.Forging temperature during forge hot is preferably set to more than 180 DEG C and is less than 280 DEG C.
In addition, if a deflection direction is forged, then what strain gathers deflection direction, and the grain shape after especially solution treatment operation S5 is stretched along major axis side, and crystal grain diameter is greater than 10 than sometimes.If become like this, then Al forges the hot properties decline of material, and the Al that can not manufacture hot properties excellence forges material.In order to control below 10 by crystal grain diameter ratio, suppress the forging method straining the deflection gathered to be effective, forging (that is, more than two sides forging) more than both direction is effective.
The microtexture of Al alloy after solution treatment is subject to significantly affecting of the forging ratio of forge hot.Therefore, in order to Al is forged material solution treatment after microtexture be controlled to illustrated crystal grain diameter and the shape of crystal grain, forging ratio is set to more than 1.5.If forging ratio is less than 1.5, then the tissue of Al alloy easily forms mixing crystal grain.In addition, a direction is not only in the direction of forging, at least carry out more than different both direction (sometimes also referred to as two sides forging), preferably three directions (sometimes also referred to as three forgings), the forging ratio in preferred all directions is more than 1.5.At this, two sides forging, three forgings are described.
Carry out two sides forging, three casting materials forged can be rectangular parallelepiped, cubes, right cylinder etc.It should be noted that, in rectangular parallelepiped, cubical situation, can before forge hot, carry out blocking or cut, be formed thus.
Such as, when the casting material of rectangular parallelepiped, there is A face, the B face vertical with this A face and the C face vertical with B face with this A face.That is, when casting material using A face as upper surface, be made up of A face, the face relative with this A face (lower surface), side B, the face relative with this side B, C face and these six, the face relative with this C face.
Such as, B face and this two sides, C face are forged, make the area in A face reach 1/2 (forging ratio in A face is 2S).Then, A face and this two sides, C face are forged, make the area in B face reach 1/2 (forging ratio in B face is 2S).Forging is hereto called two sides forging.
Further, A face and this two sides, B face are forged, make the area in C face reach 1/2 (forging ratio in C face is 2S).Forging is hereto called three forgings.
In the present invention, can two sides forging or three forgings be set as once, the forging of above two sides or three forgings can also be carried out once.The upper limit of forging does not have special stipulation, and the size according to desired forging material decides.It should be noted that, after carrying out the forging of one or many two sides or three forgings, can carry out the forging (that is, also can forge for four sides forging, five forgings, six sides forging, seven forgings, octahedrals) of arbitrary face once or twice, this is from saying.
So, by forging at least two sides of casting material, the orientation (can make it even) of the strength of materials or elimination crystal grain can be increased, thus can improve fatigue strength in high temperature environments.
(die forging operation)
Die forging operation S4 is the optional operation can carried out between hot forging process S3 and solution treatment operation S5, is the operation of forging material being carried out die forging the die forging temperature of 180 ~ 360 DEG C.
According to the shape etc. of product, also can select to carry out die forging operation S4 after above-mentioned hot forging process S3.Even if in this die forging operation S4, temperature condition during forging is also important for realizing improving for the characteristic of Al alloy, fatigue strength especially in high temperature environments.That is, be important for the shape of the crystal grain diameter after the solution treatment operation S5 of control Al alloy and crystal grain.
In addition, same with above-mentioned hot forging process S3, if forging deflection direction, then what strain gathers deflection direction, and the grain shape after especially solution treatment operation S5 is stretched along major axis side, and crystal grain diameter is greater than 10 than sometimes.If become like this, then Al forge material hot properties decline, can not reproducibility manufacture well hot properties excellence Al forge material.In order to crystal grain diameter ratio is controlled below 10, in die forging operation S4, in order to a direction is not partial in forging direction when making die forging, suitably study and apply the suppression such as adjustment mold shape to strain the die forging scheme gathering deflection be effective.
Same with above-mentioned forge hot, by forging temperature during die forging is set to 180 ~ 360 DEG C, the shape of crystal grain diameter and crystal grain can be controlled, and stably can manufacture Al forging material.When the forging temperature of die forging is less than 180 DEG C, when die forging, Al forging material easily produces and breaks, and forging processing itself is difficult.On the other hand, if the forging temperature of die forging is greater than 360 DEG C, then Al forges in the tissue of material and easily produces coarse grain.Therefore, Al forge material hot properties decline, can not reproducibility manufacture well hot properties excellence Al forge material.Therefore, forging temperature during die forging is preferably set to 180 ~ 360 DEG C, is more preferably set to more than 180 DEG C and is less than 280 DEG C.
(solution treatment operation and quench treatment operation)
Then, solution treatment operation S5 and quench treatment operation S6 is described.
Solution treatment operation S5 will carry out the maintenance temperature of the forging material after forge hot at 510 ~ 545 DEG C and carry out the operation of solution treatment.
In addition, the forging material after carrying out solution treatment is more than 10 DEG C/min with the average cooling rate between 400 ~ 290 DEG C and the condition being less than 30000 DEG C/min carries out the operation of quench treatment by quench treatment operation S6.
In this solution treatment operation S5 and quench treatment operation S6, in order to make the solid solution suppress separating out again in cooling as far as possible again of compound between soluble metal, preferably carry out in the defined terms such as JIS-H-4140, AMS-H-6088.But, even if heat-treat according to standards such as AMS-H-6088, if solid solution temperature is too high, then also there is burning, mechanical property significantly declined.Otherwise if solid solution temperature is below lower limit temperature, then the yield strength after artificial age-hardening's process is insufficient for object of the present invention, and solution treatment itself also becomes difficulty.Therefore, the upper limit of solid solution temperature is set to 545 DEG C, lower limit is set to 510 DEG C.
Stove for solution treatment and quench treatment etc. modified (thermal treatment) suitably can use batch furnace, continuous annealing furnace, melting salt liquid furnace, oil oven etc.In addition, cooling way during quenching also suitably can select the method such as water retting, warm water immersion, boiling water dipping, polymer liquid dipping, jet of water, air spray.It should be noted that, the polymkeric substance for polymer liquid dipping can use polyoxyethylene-propylene-polyethers etc.Specifically, the UCONQuenchant (trade(brand)name) of U.S. combinating carbide (UnionCarbide) Inc. can such as be used.
Quench treatment operation S6 makes θ ' phase, Ω phase fine and separate out to high-density in (100) face of Al alloy, (111) face when the artificial age-hardening of the high temperature carried out subsequently processes, and is to forge the intensity of material and the operation wanted of overstating for the Al after improving artificial age-hardening's process.In quench treatment, if the average cooling rate between 400 ~ 290 of process of cooling DEG C is slow, then separate out thick θ ' phase, Ω phase in cooling way, the strength of materials after artificial age-hardening's process declines.In addition, the size of actual product (Al forges material) is wide reaches tens of mm ~ number m, and quenching wall thickness differs widely.Therefore, the working conditions according to product, environment for use is needed suitably to adjust the speed of cooling in quench treatment.Study for various product, found that, if the average cooling rate between 400 ~ 290 of process of cooling DEG C is less than 10 DEG C/min, then the strength of materials declines, and can not meet fatigue strength in high temperature environments.In addition, speed of cooling is faster then more effective to raising intensity, therefore fast better off, if but more than 30000 DEG C/min, be then difficult to control quenching velocity.Therefore, the average cooling rate between 400 ~ 290 DEG C preferably with more than 10 DEG C/min and the condition being less than 30000 DEG C/min carry out.The lower limit of the average cooling rate between 400 ~ 290 DEG C is such as preferably 15 DEG C/min, is more preferably 20 DEG C/min.In addition, be just not particularly limited as long as the upper limit of average cooling rate between 400 ~ 290 DEG C is less than 30000 DEG C/min, but be such as more preferably 20000 DEG C/min, more preferably 10000 DEG C/min, and then be more preferably 6000 DEG C/min.
((processing) operation of colding pressing)
(processing) the operation S7 that colds pressing is the optional operation can carried out after quench treatment operation S6.Cold pressing if carry out (processing) operation S7, then can correcting quenching process time strain, the hot properties such as the yield strength of the finished product, creep rupture strength can be made to improve.Cold pressing (processing) cold-rolling mill, striking-out machine and cold forging etc. can be used.If cold pressing, the compression (processing) of (processing) is measured little, then can not get the effect of enough reduction residual stresss.On the other hand, if compression (processing) amount of cold pressing (processing) is large, then forge material in artificial age-hardening's process or by Al when using in high temperature environments, because the amount of precipitation of θ ' phase increases, yield strength easily declines.Therefore, (processing) preferred compressed (processing) rate of colding pressing is set to 1 ~ 5%.
(T6 is modified)
Even if the residual stresss such as the small members of diameter to about 100mm, piston are comparatively large, also problem can not be become in the processing such as cutting.Therefore, under such circumstances, preferably after solution treatment and quench treatment are carried out to Al forging material, implement artificial age-hardening's process, form modified T6 material.Now, even if also obtain high-strength characteristic and hot properties comparatively greatly in order to residual stress, preferably the temperature of quench treatment is set to less than 50 DEG C.
(T61 is modified)
For the large products such as rotary blade, when quench treatment, the speed of cooling of product surface and central part differs widely, and therefore produces on the surface of product (Al forges material) and is greater than about 98MPa (10kgf/mm 2) high residue stress.If the surface of forging material at Al produces residual stress high like this, then produce large strain when Al forges the machining of material, accurate machining becomes very difficulty.In addition, according to circumstances, sometimes in machining, also likely produce breaking of causing because of residual stress, thus the destruction that Al forges material occurs.Even if not break in machining etc., Al forges the destruction of material, in the life-time service of product crackle easily with material in the intermetallic compound such as residual crystallisate for starting point or the tiny area damage that produces in transmitting with product etc. for starting point carries out propagations growth, also likely finally cause destruction.
Therefore, the residual stress for rotary blade etc. becomes the product of problem, in order to residual stress be removed or be reduced to preferably about 29MPa (3.0kgf/mm 2) below, preferably the water quenching temperature after solution treatment is set to the relatively-high temperature of more than 70 DEG C, implement artificial age-hardening's process afterwards, form modified T61 material.
(T652 is modified)
According to the purposes of product (Al forges material), no matter the equal stringent regulations residual stress of the size of product sometimes.For such product, in order to reduce residual stress as far as possible, preferably apply to cold pressing (processing), residual stress is removed or is reduced to preferably about 29MPa (3.0kgf/mm 2) below, implement artificial age-hardening's process and form modified T652 material.In order to form modified T652 material, such as preferred quenching temperature is set to less than 50 DEG C.
It should be noted that, if cold pressing (processing) of cold pressing (processing) measures little, even then quenching temperature is set to the situation of less than 50 DEG C, the effect of enough reduction residual stresss can not be obtained.On the other hand, if (processing) amount of colding pressing is large, even then quenching temperature to be set to the situation of less than 50 DEG C, in use in artificial age-hardening's process or at high temperature, the amount of precipitation of θ ' phase increases, and therefore yield strength easily declines.Therefore, cold pressing (processing) preferably will compress (processing) rate and be set to 1 ~ 5%.
(artificial age-hardening's treatment process)
Artificial age-hardening treatment process S8 is the operation of carrying out after quench treatment operation S6.It should be noted that, when carrying out colding pressing (processing) operation S7 after quench treatment operation S6, at this (processing) operation S7 laggard row artificial aging hardening treatment operation S8 that colds pressing.Artificial age-hardening treatment process S8 is the operation that forging material to carrying out quench treatment, after cold pressing (processing) carries out artificial age-hardening's process.
Above-mentioned each modified in the hot properties such as normal temperature yield strength, high-temperature yield strength, creep rupture strength of material is forged in artificial age-hardening's process in order to give Al, fatigue strength in high temperature environments carries out.The Ω phase separated out in (111) face of Al alloy can be made to separate out mutually with the θ ' separated out in (100) face by this artificial age-hardening process, thus show above-mentioned characteristic.The method of artificial age-hardening's process is not particularly limited, as long as forge in material at Al of the present invention, Ω phase and θ ' form the precipitation state of the fatigue strength met in high temperature environments mutually, as long as preferably can obtain hot properties and the metal fatigue characteristics such as normal temperature yield strength, high-temperature yield strength, creep rupture strength.
Above, an embodiment of Al forging material of the present invention and manufacture method thereof is illustrated.
Forge material according to Al of the present invention, because average crystal grain diameter is less than 500 μm, crystal grain diameter ratio (major axis/minor axis) is less than 10, and fatigue strength in high temperature environments therefore can be made excellent.
Forge the manufacture method of material according to Al of the present invention, the Al that average crystal grain diameter is less than 500 μm, crystal grain diameter ratio (major axis/minor axis) is less than 10 can be manufactured and forge material.Therefore, forge the manufacture method of material according to Al of the present invention, the Al that can manufacture fatigue strength excellence in high temperature environments forges material.
Embodiment
Then, based on embodiment, the present invention will be described.It should be noted that, the invention is not restricted to embodiment shown below.
(test material 1 ~ 23)
Use the Al alloy shown in composition 1 ~ 17 of table 1, the ingot casting (diameter 500mm × length 2000mm) of the test material 1 ~ 23 of table 2 is carried out melting.Afterwards, the thermal treatment that homogenizes (air furnace) of 510 DEG C × 15 hours is implemented.Further, in order to adjust average crystal grain diameter and crystal grain diameter ratio, utilize forge hot with the forging ratio in all directions be more than 1.5 mode three forgings are carried out to the ingot casting after the thermal treatment that homogenizes.It should be noted that, the forging temperature of forge hot sets between 180 ~ 360 DEG C.Then, make (cutting) by mechanical workout and make the material of the length of square (the thickness) × 300mm of 50mm by the forging materials having carried out three forgings.This cutting material is heated up with rate of heating 200 DEG C/h in air furnace, after carrying out the solution treatment of 530 DEG C × 3 hours, carry out warm water quenching (average cooling rate about 30 ~ 120 DEG C/min) of 70 ~ 91 DEG C, implement artificial age-hardening's process of 190 DEG C × 18 hours, make test material 1 ~ 23 (being modified T61 material).
It should be noted that, for test material 14, the forging temperature of forge hot is changed to 400 DEG C, for test material 15, made test material with the forging (one side forging) in a direction.
It should be noted that, in the composition shown in table 1, surplus is Al and inevitable impurity.The numeric representation that table 1 acceptance of the bid pours down line does not meet important document of the present invention.
[table 1]
For made each test material, as following, measure average crystal grain diameter and crystal grain diameter ratio, measure fatigue strength in high temperature environments.
(mensuration of average crystal grain diameter, crystal grain diameter ratio)
As shown in Figure 2, cut the sample of measurement site with the size of about 15mm × 15mm × 10 ~ 20mm from test material, carry out imbedding resin.Further, grinding is carried out to carry out electrolytically etching to the face imbedding the sample after resin, has carried out photograph taking by opticmicroscope.Multiplying power during photograph taking and the size of crystal grain diameter correspondingly adjust arbitrarily.
The mensuration of crystal grain diameter is undertaken by so-called section method.That is, the mensuration of crystal grain diameter as shown in Figure 3, respectively marks 3 lines (a1 ~ a3 of Fig. 3, b1 ~ b3) respectively equably at the vertical and horizontal of optical microscope photograph, measures the quantity of the crystal boundary that every root passes through.Crystal grain diameter calculates according to the quantity of the multiplying power of photo, size and crystal boundary.A series of mensuration is carried out with three photos, according to the mensuration of vertical 9 (namely 3 × 3), horizontal 9 (namely 3 × 3), obtain the crystal grain diameter of N=9 respectively in length and breadth, calculate the average of crystal grain diameter respectively according to longitudinal and transverse, obtain longitudinal and transverse respective average crystal grain diameter.Further, further longitudinal and transverse respective average crystal grain diameter is added and after calculate that it is average, thus as average crystal grain diameter.
In addition, crystal grain diameter ratio (major axis/minor axis) obtains as follows: the mean value using longitudinal and transverse respective crystal grain diameter, by larger for crystal grain diameter being set to major axis, less being set to minor axis, calculates crystal grain diameter ratio.
(fatigue strength in high temperature environments)
Make following test film by the modified material of made T61, this test film is carried out Fatigue Strength of Metal test (maximum stress 130MPa, stress ratio-1) under the hot environment of 150 DEG C.For test film, be 6mm by the diameter being set as parallel portion, the length of parallel portion be 13.55mm and the pole test film carried out after the sand paper polishing of #1000 for rotary bending fatigue strength trial.
The measurement result of rotary bending fatigue strength trial, i.e. multiplicity of breaking are shown in table 2.It should be noted that, the multiplicity of repeatedly returning and counting and referring in rotation fatigue test to breaking of breaking.In addition, the numeric representation that table 2 acceptance of the bid pours down line does not meet important document of the present invention.
Multiplicity of breaking is less than 5.0e 6(be less than 5.0 × 10 6) be evaluated as "×", 5.0e 6above and be less than 8.0e 6(5.0 × 10 6above and be less than 8.0 × 10 6) be evaluated as " △ ", 8.0e 6above (8.0 × 10 6above) be evaluated as "○".In the present invention, "○" is qualified, and " △ " and "×" are defective.
[table 2]
As shown in table 2, test material 1 ~ 13,20 ~ 23 meets important document of the present invention, thus fatigue strength in high temperature environments good (embodiment).
On the other hand, test material 14 ~ 19 does not meet important document of the present invention, thus becomes the result (comparative example) that fatigue strength is in high temperature environments bad.
Specifically, test material 14 due to the condition of forging temperature be 400 DEG C, thus average crystal grain diameter does not meet important document of the present invention.Its result, test material 14 becomes the bad result of fatigue strength in high temperature environments.
Test material 15 makes owing to utilizing the forging in a direction, and therefore crystal grain diameter ratio (major axis/minor axis) does not meet important document of the present invention.Its result, test material 15 becomes the bad result of fatigue strength in high temperature environments.
Test material 16, because the content of Cu is lower than lower value, thus can not obtain the sufficient strength of materials, becomes the result that fatigue strength is in high temperature environments bad.
Test material 17 is less than lower value due to the content of Mg, thus can not obtain the sufficient strength of materials, becomes the result that fatigue strength is in high temperature environments bad.
Test material 18 is because the content of Mn is lower than lower value, and thus crystal grain diameter becomes large, can not obtain sufficient fatigue strength.Therefore, test material 18 and become the bad result of fatigue strength in high temperature environments.
Test material 19, because the content of Ag is lower than lower value, thus fails to make the width of PFZ become enough narrow.Therefore, test material 19 and become the bad result of fatigue strength in high temperature environments.
(test material 24)
Then, the Al alloy shown in composition 1 of use table 1 has made test material 24.Test material 24 is except 2 three forgings except carrying out forging ratio in all directions, and material 1 is same makes with test.
For made test material 24, rotary bending fatigue strength trial is carried out with condition similar to the above, fatigue strength is in high temperature environments evaluated, result and test material 1 ~ 13,20 ~ 23 same fatigue characteristic (embodiment) met under 150 DEG C of such hot environments.
(test material 25 ~ 35)
Then, as shown in table 3, except using composition 1, also the hot forging temperature (DEG C) shown in his-and-hers watches 3 and the average cooling rate (DEG C/min) between 400 ~ 290 DEG C after carrying out solution treatment have carried out, except control, having made test material 25 ~ 35 in the same manner as test material 1 respectively.
Further, for test material 25 ~ 35, carry out rotary bending fatigue strength trial with condition similar to the above, determine fatigue strength in high temperature environments.
The evaluation result of fatigue strength in high temperature environments of test material 25 ~ 35 and hot forging temperature (DEG C) and average cooling rate (DEG C/min) are together shown in Table 3.It should be noted that, the numeric representation that table 3 acceptance of the bid pours down line does not meet important document of the present invention.
[table 3]
Test material 25 ~ 32 meets important document of the present invention and (is average crystal grain diameter less than 500 μm, crystal grain diameter ratio (major axis/minor axis) is also less than 10), therefore as shown in table 3, fatigue strength in high temperature environments good (embodiment).Especially, test material 26,30 due to the average cooling rate between 400 ~ 290 after carrying out solution treatment DEG C large, therefore tensile strength high (not being shown in Table 3).
On the other hand, test material 33 ~ 35, owing to not meeting important document of the present invention, therefore becomes the result (comparative example) that fatigue strength is in high temperature environments bad.
Specifically, test material 33,34 is greater than the upper limit due to hot forging temperature, and thus crystal grain diameter becomes large (average crystal grain diameter is greater than 500 μm), does not obtain sufficient fatigue strength.Therefore, test material 33,34 and become the bad result of fatigue strength in high temperature environments.
Test material 35, because average cooling rate is lower than lower limit, does not thus obtain the sufficient strength of materials (yield strength is less than 350MPa), does not obtain sufficient fatigue strength.Therefore, test material 35 and become the bad result of fatigue strength in high temperature environments.
(test material 36)
Then, use the Al alloy shown in composition 1 of table 1, carry out as the forging ratio in all directions of forge hot be 2 three forgings, made test material 36.Test material 36 is except carrying out except the die forging close to disc-shape at 270 DEG C after forge hot, and material 1 is same makes with test.
For made test material 36, rotary bending fatigue strength trial is carried out with condition similar to the above, fatigue strength is in high temperature environments evaluated, result and test material 1 ~ 13,20 ~ 23 same fatigue characteristic (embodiment) met under 150 DEG C of such hot environments.
Nomenclature
S1 casting process
S2 homogenizes heat treatment step
S3 hot forging process
S4 die forging operation
S5 solution treatment operation
S6 quench treatment operation
Operation that S7 colds pressing (processing)
S8 artificial age-hardening treatment process

Claims (8)

1. an aluminum alloy forged material, it is characterized in that, it is the aluminum alloy forged material that will undertaken forging by Al and aluminium alloy that inevitably impurity is formed containing Cu:3.0 ~ 8.0 quality %, Mg:0.01 ~ 2.0 quality %, Ag:0.05 ~ 1.0 quality %, Mn:0.05 ~ 1.5 quality % and surplus and be formed, its average crystal grain diameter is less than 500 μm, and crystal grain diameter ratio and major axis/minor axis are less than 10.
2. aluminum alloy forged material according to claim 1, it is characterized in that, described aluminium alloy contains one or more the element be selected from Zn:0.01 ~ 0.40 quality %, Si:0.01 ~ 1.00 quality %, V:0.01 ~ 0.15 quality %, Cr:0.01 ~ 0.30 quality %, Zr:0.01 ~ 0.50 quality %, Sc:0.01 ~ 1.00 quality % and Ti:0.01 ~ 0.20 quality %.
3. a manufacture method for aluminum alloy forged material, is characterized in that, it comprises:
Casting process, melts the aluminium alloy be made up of forming shown in claim 1 or claim 2 and is cast as casting material;
Homogenize heat treatment step, to homogenize thermal treatment to described casting material the maintenance temperature of 500 ~ 545 DEG C;
Hot forging process, carries out to the heat treated casting material that homogenizes described in having carried out the forge hot that forging ratio is more than 1.5 the forging temperatures of 180 ~ 360 DEG C;
Solution treatment operation, carries out solution treatment the maintenance temperature of 510 ~ 545 DEG C to the forging material carrying out described forge hot;
Quench treatment operation, is more than 10 DEG C/min with the average cooling rate between 400 ~ 290 DEG C and the condition being less than 30000 DEG C/min carries out quench treatment to the forging material carrying out described solution treatment; And
Artificial age-hardening's treatment process, carries out artificial age-hardening's process to the forging material carrying out described quench treatment.
4. the manufacture method of aluminum alloy forged material according to claim 3, is characterized in that, described forge hot is forged two different faces of described casting material at least successively.
5. the manufacture method of aluminum alloy forged material according to claim 3, is characterized in that, described forge hot is forged three different faces of described casting material successively.
6. the manufacture method of the aluminum alloy forged material according to any one of claim 3 ~ 5, is characterized in that, described forging temperature is decided to be more than 180 DEG C and is less than 280 DEG C.
7. the manufacture method of the aluminum alloy forged material according to any one of claim 3 ~ 5, it is characterized in that, the die forging temperature being included in 180 ~ 360 DEG C between described hot forging process and described solution treatment operation carries out the die forging operation of die forging to described forging material.
8. the manufacture method of aluminum alloy forged material according to claim 7, is characterized in that, described die forging temperature is decided to be more than 180 DEG C and is less than 280 DEG C.
CN201510523468.3A 2014-10-16 2015-08-24 Aluminum alloy forged material and its manufacture method Expired - Fee Related CN105525170B (en)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
JP2014211865A JP2016079454A (en) 2014-10-16 2014-10-16 Aluminum alloy forging material and manufacturing method therefor
JP2014-211865 2014-10-16

Publications (2)

Publication Number Publication Date
CN105525170A true CN105525170A (en) 2016-04-27
CN105525170B CN105525170B (en) 2017-07-21

Family

ID=54260604

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201510523468.3A Expired - Fee Related CN105525170B (en) 2014-10-16 2015-08-24 Aluminum alloy forged material and its manufacture method

Country Status (4)

Country Link
EP (1) EP3009525A1 (en)
JP (1) JP2016079454A (en)
KR (1) KR101792342B1 (en)
CN (1) CN105525170B (en)

Cited By (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106321779A (en) * 2016-08-26 2017-01-11 宁波市鄞州唯达汽车配件厂（普通合伙） Gear case of cutting machine
CN107999687A (en) * 2017-11-29 2018-05-08 无锡透平叶片有限公司 A kind of aluminium alloy vane forging and preparation method thereof
CN108103373A (en) * 2017-12-28 2018-06-01 中南大学 A kind of argentiferous Al-Cu-Mg alloy and the heat treatment method for obtaining high intensity P texture
CN108913963A (en) * 2018-06-22 2018-11-30 镇江市益宝电气科技有限公司 A kind of high-strength corrosion-resisting bus duct
CN109055838A (en) * 2018-09-11 2018-12-21 湖南工业大学 A kind of high tough aluminum alloy materials and its application in terms of preparing shell case
CN110586826A (en) * 2019-09-12 2019-12-20 广东长盈精密技术有限公司 Preparation method of aluminum alloy shell
CN111101038A (en) * 2019-12-20 2020-05-05 山东南山铝业股份有限公司 Multi-element heat-resistant aluminum alloy and preparation method thereof
CN111321330A (en) * 2020-02-25 2020-06-23 山东南山铝业股份有限公司 Scandium-containing Al-Cu heat-resistant aluminum alloy and preparation method thereof
CN111532080A (en) * 2019-02-06 2020-08-14 Bbs日本株式会社 Aluminum alloy forged wheel, method for manufacturing same, and cast slab for forming forged wheel
CN112207522A (en) * 2020-10-26 2021-01-12 许晨玲 Flatness control method for large aluminum alloy integral wall plate
CN114134370A (en) * 2021-10-29 2022-03-04 湖南文昌新材科技股份有限公司 High-strength heat-resistant aluminum-based composite material and preparation method thereof
CN114855039A (en) * 2021-02-03 2022-08-05 中国石油化工股份有限公司 Al-Cu-Mg-Ag alloy and preparation method and application thereof

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
BR112021008854A2 (en) * 2018-11-16 2021-08-17 Arconic Technologies Llc 2xxx aluminum alloys
KR102487222B1 (en) * 2021-03-18 2023-01-12 (주) 동양에이.케이코리아 High-strength aluminum rolled plate manufacturing method and high-strength aluminum rolled plate using the same
CN113649768B (en) * 2021-08-05 2023-03-14 陕西斯瑞新材料股份有限公司 Manufacturing method of Cu-Cr alloy rotor end ring of squirrel-cage asynchronous traction motor for rail transit
CN114160748A (en) * 2021-12-15 2022-03-11 陕西宏远航空锻造有限责任公司 Forging method and device for improving structure uniformity of 2A70 alloy annular forging
CN114210894A (en) * 2021-12-27 2022-03-22 内蒙古北方重工业集团有限公司 Forging temperature control method for 35CrNi3Mo die cast ingot precision forging machine

Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000119786A (en) * 1998-10-07 2000-04-25 Kobe Steel Ltd Aluminum alloy forging material for high speed motion part
JP2004002987A (en) * 2002-03-29 2004-01-08 Kobe Steel Ltd Aluminum alloy material for forging superior in high-temperature property
JP2005082816A (en) * 2003-09-04 2005-03-31 Kobe Steel Ltd Aluminum alloy forging excellent in high temperature fatigue strength
JP2007239029A (en) * 2006-03-09 2007-09-20 Furukawa Sky Kk Malleable heat-resistant aluminum alloy
CN101437968A (en) * 2006-05-18 2009-05-20 株式会社神户制钢所 Method for producing aluminum alloy thick plate, and aluminum alloy thick plate
JP2013142168A (en) * 2012-01-11 2013-07-22 Furukawa-Sky Aluminum Corp Aluminum alloy excellent in creep resistance
CN103459630A (en) * 2011-06-10 2013-12-18 株式会社神户制钢所 Aluminum alloy having excellent high-temperature characteristics

Family Cites Families (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2001181771A (en) * 1999-12-20 2001-07-03 Kobe Steel Ltd High strength and heat resistant aluminum alloy material
JP2002206134A (en) * 2000-10-03 2002-07-26 Kobe Steel Ltd Aluminum alloy extrusion material having excellent intergranular corrosion resistance, apparatus and thermostatic refrigerant expansion valve composing refrigeration cycle using the extrusion material
US8043445B2 (en) * 2003-06-06 2011-10-25 Aleris Aluminum Koblenz Gmbh High-damage tolerant alloy product in particular for aerospace applications
DE60309711T2 (en) * 2003-09-26 2007-09-13 Kabushiki Kaisha Kobe Seiko Sho, Kobe Aluminum alloy forging material with excellent high temperature fatigue strength
JP2006213942A (en) * 2005-02-01 2006-08-17 Kobe Steel Ltd Aluminum alloy extruded shape material for rear side rail having excellent corrosion resistance
JP5698695B2 (en) * 2012-03-30 2015-04-08 株式会社神戸製鋼所 Aluminum alloy forgings for automobiles and manufacturing method thereof

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2000119786A (en) * 1998-10-07 2000-04-25 Kobe Steel Ltd Aluminum alloy forging material for high speed motion part
JP2004002987A (en) * 2002-03-29 2004-01-08 Kobe Steel Ltd Aluminum alloy material for forging superior in high-temperature property
JP2005082816A (en) * 2003-09-04 2005-03-31 Kobe Steel Ltd Aluminum alloy forging excellent in high temperature fatigue strength
JP2007239029A (en) * 2006-03-09 2007-09-20 Furukawa Sky Kk Malleable heat-resistant aluminum alloy
CN101437968A (en) * 2006-05-18 2009-05-20 株式会社神户制钢所 Method for producing aluminum alloy thick plate, and aluminum alloy thick plate
CN103459630A (en) * 2011-06-10 2013-12-18 株式会社神户制钢所 Aluminum alloy having excellent high-temperature characteristics
JP2013142168A (en) * 2012-01-11 2013-07-22 Furukawa-Sky Aluminum Corp Aluminum alloy excellent in creep resistance

Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106321779A (en) * 2016-08-26 2017-01-11 宁波市鄞州唯达汽车配件厂（普通合伙） Gear case of cutting machine
CN107999687A (en) * 2017-11-29 2018-05-08 无锡透平叶片有限公司 A kind of aluminium alloy vane forging and preparation method thereof
CN108103373A (en) * 2017-12-28 2018-06-01 中南大学 A kind of argentiferous Al-Cu-Mg alloy and the heat treatment method for obtaining high intensity P texture
CN108103373B (en) * 2017-12-28 2019-11-19 中南大学 A kind of argentiferous Al-Cu-Mg alloy and the heat treatment method for obtaining high intensity P texture
CN108913963A (en) * 2018-06-22 2018-11-30 镇江市益宝电气科技有限公司 A kind of high-strength corrosion-resisting bus duct
CN109055838A (en) * 2018-09-11 2018-12-21 湖南工业大学 A kind of high tough aluminum alloy materials and its application in terms of preparing shell case
CN111532080B (en) * 2019-02-06 2023-04-21 Bbs日本株式会社 Aluminum alloy forged wheel, manufacturing method thereof, and casting blank for forming forged wheel
CN111532080A (en) * 2019-02-06 2020-08-14 Bbs日本株式会社 Aluminum alloy forged wheel, method for manufacturing same, and cast slab for forming forged wheel
CN110586826A (en) * 2019-09-12 2019-12-20 广东长盈精密技术有限公司 Preparation method of aluminum alloy shell
CN111101038A (en) * 2019-12-20 2020-05-05 山东南山铝业股份有限公司 Multi-element heat-resistant aluminum alloy and preparation method thereof
CN111321330A (en) * 2020-02-25 2020-06-23 山东南山铝业股份有限公司 Scandium-containing Al-Cu heat-resistant aluminum alloy and preparation method thereof
CN111321330B (en) * 2020-02-25 2022-04-01 山东南山铝业股份有限公司 Scandium-containing Al-Cu heat-resistant aluminum alloy and preparation method thereof
CN112207522A (en) * 2020-10-26 2021-01-12 许晨玲 Flatness control method for large aluminum alloy integral wall plate
CN114855039A (en) * 2021-02-03 2022-08-05 中国石油化工股份有限公司 Al-Cu-Mg-Ag alloy and preparation method and application thereof
CN114134370A (en) * 2021-10-29 2022-03-04 湖南文昌新材科技股份有限公司 High-strength heat-resistant aluminum-based composite material and preparation method thereof
WO2023070739A1 (en) * 2021-10-29 2023-05-04 湖南文昌新材科技股份有限公司 High-strength heat-resistant aluminum-based composite material and preparation method therefor

Also Published As

Publication number Publication date
KR101792342B1 (en) 2017-11-01
KR20160045021A (en) 2016-04-26
EP3009525A1 (en) 2016-04-20
JP2016079454A (en) 2016-05-16
CN105525170B (en) 2017-07-21

Similar Documents

Publication Publication Date Title
CN105525170A (en) Aluminium alloy forging and method for producing the same
JP5652730B1 (en) Ni-base superalloy and manufacturing method thereof
CN103459630B (en) The aluminium alloy of hot properties excellence
CN104775062B (en) High-strength aluminum-alloy material, aluminum-alloy plate and manufacturing method thereof
KR102224687B1 (en) Rolling and preparation method of magnesium alloy sheet
CN104342590B (en) Aluminum alloy extrudate for cutting
JP2018534435A (en) Aluminum alloy
NO143166B (en) PROCEDURE FOR MANUFACTURING DISPERSION-STRENGTHED ALUMINUM ALLOY PRODUCTS
JP2000119786A (en) Aluminum alloy forging material for high speed motion part
CN106148784B (en) A kind of low cost room temperature high-ductility wrought magnesium alloy material and its preparation process
EP2274454A1 (en) Alloy composition and preparation thereof
WO2015151808A1 (en) METHOD FOR PRODUCING Fe-Ni-BASED SUPER HEAT-RESISTANT ALLOY
CN107614718A (en) High-strength aluminum alloy hot forging material
US10125410B2 (en) Heat resistant aluminum base alloy and wrought semifinsihed product fabrication method
CN104775059B (en) Al-Mg-Si series aluminum-alloy material with long-time natural aging stability, aluminum-alloy plate and manufacturing method thereof
JP2006257522A (en) Al-Zn-Mg-Cu-BASED ALUMINUM ALLOY CONTAINING ZR AND METHOD FOR MANUFACTURING THE SAME
JP3548709B2 (en) Method for producing semi-solid billet of Al alloy for transportation equipment
JP6063318B2 (en) Aluminum alloy and method for producing the same
JP4088546B2 (en) Manufacturing method of aluminum alloy forging with excellent high temperature characteristics
JP2001181771A (en) High strength and heat resistant aluminum alloy material
CN105200283A (en) New process avoiding coarse 6063 extrusion aluminum alloy crystals
EP1522600B1 (en) Forged aluminium alloy material having excellent high temperature fatigue strength
Zhou et al. Effects of aging temperature on the microstructure and mechanical properties of a Ti2AlNb based alloy
RU2299264C1 (en) Deformed aluminum alloys articles forming method
KR101292191B1 (en) The method for preparation of Mg alloy sheet using different speed rolling and magnesium alloy sheet using the same

Legal Events

Date Code Title Description
C06 Publication
PB01 Publication
C10 Entry into substantive examination
SE01 Entry into force of request for substantive examination
GR01 Patent grant
CF01 Termination of patent right due to non-payment of annual fee
CF01 Termination of patent right due to non-payment of annual fee

Granted publication date: 20170721

Termination date: 20200824