CN104946934A - Aluminum alloy forging material for welding structure member and method for manufacturing same - Google Patents
Aluminum alloy forging material for welding structure member and method for manufacturing same Download PDFInfo
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Abstract
The invention provides an aluminum alloy forging material for a welding structure member and a method for manufacturing the same, wherein the aluminum alloy forging material can maintain the tensile strength, and is excellent in weld crack resistance and stress corrosion crack resistance. The aluminum alloy forging material (1) for the welding structure member is characterized in that in the structure of the aluminum alloy forging material (1) for the welding structure member, two of three faces, observed in a position having a shear band, in orthogonal directions can be represented by the following form: 50 <= GL <=500(1), 10 <= GS <=180(2) and GS <=GL(3), when the length of a grain in a long axial direction is assumed as GL [mu]m, the length of the grain in a short axial direction is GS [mu]m, and a grain (4) bends in a long axial direction of the residual face.
Description
Technical field
The present invention relates to the aluminum alloy forged material and manufacture method thereof that are suitable for welded construction parts.
Background technology
As the structure unit of the carrier vehicle of automobile, motorcycle, rail truck, aircraft etc., widely use such as high strength, the 7000 line aluminium alloy materials that erosion resistance is also excellent.(following, " aluminium alloy " is described as " Al alloy ".)
Using as 7000 be the representational alloy of Al alloy 7N01 based on Al alloy forging material, through following operation manufacture: after carrying out forge hot with the temperature of 350 ~ 500 DEG C, solution treatment is carried out with the temperature of 400 ~ 500 DEG C, thereafter do not carry out natural aging treatment, and carry out artificial aging process and manufacture.
Such as in patent documentation 1, disclose a kind of manufacture method of Al alloy forging goods, it is characterized in that, comprise following operation: the operation obtaining the former material of Al alloy forging containing, for example lower alloy composition, this alloy composition contains Fe:0.2 ~ 0.35 quality %, Cu:0.05 ~ 0.20 quality %, Mn:0.3 ~ 0.6 quality %, Mg:1.3 ~ 2.0 quality %, Zn:4.6 ~ 5.1 quality %, Si: lower than 0.30 quality %, more than Zr:0.1 quality % and with the total amount of Ti lower than 0.2 quality %, meet the relation of " [Ti quality %]/[Zr quality %] >=0.2 ", surplus is made up of Al and inevitable impurity, for the former material of described Al alloy forging, after carrying out forge hot with the temperature of 350 ~ 500 DEG C, carry out solution treatment with the temperature of 400 ~ 500 DEG C, thus obtain the operation of Al alloy forging goods, for described Al alloy forging goods, do not carry out natural aging treatment and carry out the operation of artificial aging process.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 2010-261061 publication
Invent problem to be solved
But in existing aluminum alloy forged material, when to be Al alloy using 7000 use as the forging material that can carry out welding, be Al alloy phase ratio with iron and 5000, known its is the alloy being difficult to weld.That is, 7000 is Al alloy, if suitably do not select its composition, manufacturing condition etc., then easily the defects such as welding crack occurs.
In addition, in existing aluminum alloy forged material, when vertically implementing welding from the prolonging direction of crystal grain, there is crackle easily along the problem of crystal boundary progress.
In addition, disclosed in patent documentation 1, method specify only the composition of aluminium alloy, but different according to manufacturing condition, and huge variation can occur the performance of forging material, and the reproducibility of the performance of forging material is poor.In addition, owing to fully not studying for grain-size, grain form in patent documentation 1, therefore can say according to welding conditions different, easily crackle occur.
So, about crackle during welding, up to now, fasten in the pass of grain-size and grain form and do not verify fully yet.
In addition, in aluminum alloy forged material, also require tensile strength and anticorrosion stress-resistant anti-thread breakage.In addition, in the forging material of the aluminium alloy beyond use 7000 is, require to maintain tensile strength, and proper alignment is anti-thread breakage and the characteristic of the anti-thread breakage excellence of anticorrosion stress-resistant.
Summary of the invention
The present invention completes in view of above-mentioned such situation.That is, problem of the present invention is, provides a kind of and maintains tensile strength, and proper alignment is anti-thread breakage and anticorrosion stress-resistant anti-thread breakage excellent again welded construction parts aluminum alloy forged material and manufacture method thereof.
For solving the means of problem
Therefore, there is finding out and countermeasure of the reason of crackle in the present inventor, concentrates on studies when welding to aluminum alloy forged material.
Its result draws such as the following conclusion, namely, in order to realize existing side by side of tensile strength and weldability, the crystal grain of the aluminum alloy forged material before welding is closely related with crackle when welding, by managing manufacturing condition in suitable scope, crystal grain is controlled the form for regulation, crackle when welding can be suppressed, thus reach the present invention.
Namely, welded construction parts of the present invention are (following with aluminum alloy forged material, be suitable for being called Al alloy forging material, or forging material) feature be, in the tissue of welded construction parts with aluminum alloy forged material, if the crystal grain length of major axis is GL μm, when the crystal grain length of minor axis is GS μm, among the face in orthogonal 3 directions observed at the position being formed with shear zone, two faces are expressed from the next, and its crystal grain of remaining one side has bending at long axis direction.
50≤GL≤500...(1)
10≤GS≤180...(2)
GS≤GL...(3)
By becoming the aluminum alloy forged material with this formation, maintenance tensile strength can be reached, and welding crack is difficult to occur, the aluminum alloy forged material of the anti-thread breakage excellence of anticorrosion stress-resistant.
In addition, for welded construction parts of the present invention with for aluminum alloy forged material, the aluminum alloy forged material of preferred described welded construction parts is made up of the aluminium alloy that 7000 are.
By becoming the aluminum alloy forged material with this formation, the raisings such as tensile strength, proper alignment are anti-thread breakage, anticorrosion stress-resistant is anti-thread breakage, toughness.
Welded construction parts of the present invention are the welded construction parts manufacture method of aluminum alloy forged material described above by the manufacture method of aluminum alloy forged material, it is characterized in that, carry out following operation: the casting process of the ingot casting of cast aluminium alloy; The heat treated heat treatment step that homogenizes that homogenizes is carried out for described ingot casting; The heating process of the ingot casting of heating after the described thermal treatment that homogenizes; Forge the ingot casting after described heating with 350 ~ 460 DEG C and become the forging process of forging material; Described forging material is carried out to the modified operation of T6 process or T7 process, described forging process carries out following three forging process of more than 1 time, namely the ingot casting before described forging is rectangular parallelepiped, if upper surface is A face, a side is B face, when a side adjacent with B face is C face, make the forging ratio of described each higher than 1.0S and for below 3.5S, carry out the forging in the forging in B face and C face, the forging in A face and C face, A face and B face so in order.
Utilize the manufacture method containing such operation, maintenance tensile strength can be manufactured, and welding crack is difficult to occur, the aluminum alloy forged material of the anti-thread breakage excellence of anticorrosion stress-resistant.
In forging process, particularly carry out three forgings, the tissue of forging material of the present invention, meet aforesaid formula (1) ~ (3), and become crystal grain and have bending form at long axis direction.
Invention effect
The aluminum alloy forged material of welded construction parts of the present invention maintains tensile strength, and proper alignment is anti-thread breakage and the anti-thread breakage excellence of anticorrosion stress-resistant.In addition, the welded construction parts manufacture method of aluminum alloy forged material of the application of the invention, can manufacture the above-mentioned aluminum alloy forged material of welded construction parts.
Accompanying drawing explanation
Fig. 1 is the stereographic map of the structure observation position for illustration of forging material of the present invention.
Fig. 2 is the stereographic map that the situation of the crystal grain of the inside of the forging material of the structure observation position of enlarged view 1 also schematically carries out describing.
Fig. 3 is the orthographic plan of the tissues observed in the M1 face of the forging material schematically showing Fig. 1.
Fig. 4 is the orthographic plan of the tissues observed in the M2 face of the forging material schematically showing Fig. 1.
Fig. 5 is the stereographic map of the grain structure schematically showing forging material of the present invention.
Fig. 6 is the stereographic map of the grain structure schematically showing existing forging material.
Fig. 7 is about the existing crystal grain boundary of forging material and the explanatory view of stress, is the schematic sectional view for being described crackle.
Fig. 8 is about the crystal grain boundary of forging material of the present invention and the explanatory view of stress, is the schematic sectional view for being described crackle.
Fig. 9 is being amplified in m3 face of the measuring method of GL and GS for illustration of crystal grain and schematically carries out the sectional view described.
Figure 10 is in the manufacture method for illustration of forging material of the present invention, the schematic stereographic map of three forgings in forging process.
Figure 11 is the stereographic map of the bulk of the ingot casting schematically shown before the forging material manufacturing embodiment.
Figure 12 is the schematic stereographic map of the method for welding test for illustration of embodiment.
Embodiment
Below, the embodiment of welded construction parts of the present invention by aluminum alloy forged material and manufacture method thereof is illustrated in detail.
First, forging material of the present invention is described.
(aluminum alloy forged material)
For aluminum alloy forged material, in its tissue, if the crystal grain length of major axis is GL μm, when the crystal grain length of minor axis is GS μm, among the face in mutually perpendicular 3 directions observed at the position being formed with shear zone, two faces are expressed from the next, and its crystal grain of remaining one side has bending at long axis direction.
50≤GL≤500...(1)
10≤GS≤180...(2)
GS≤GL...(3)
Formation for forging material of the present invention is described.Fig. 1 is the stereographic map of the structure observation position for illustration of forging material of the present invention, and Fig. 2 is the stereographic map that the situation of the crystal grain of the inside of the forging material of the structure observation position of enlarged view 1 also schematically carries out describing.
The M1 face of the forging material 1 shown in Fig. 1 and the tissues observed (macroscopic observation tissue) in M2 face, be presented in Fig. 3, Fig. 4 respectively.As shown in Figure 3,4, in M1 face and the M2 face of forging material 1, shear zone (main deformed region) 21 is formed with.This shear zone 21 is the parts bleached by macroetching, is formed as the band shape of white.In addition, the position beyond shear zone 21 is called dead-metal (non-deforming region) 22, is low forging tissue.Shear zone 21 is equivalent to the degree of finish region higher than dead-metal 22.By making this shear zone 21 extensively distribute, proper alignment can be improved anti-thread breakage.
Tissues observed (microscopic observation tissue) display of three of the crystal grain look-out station of the forging material 1 shown in Fig. 1 in fig. 2.Further, in Fig. 2, on paper, the face in front of being positioned at is m3 face, and the face be positioned at above is m2 face, and the face being positioned at left side is m1 face.
In addition, this look-out station as shown in Figure 3, is the position being formed with shear zone 21.
As shown in Figure 2, m1 face and m3 face, for the cross section of crystal grain 4 is elongated, the form that linearity extends.At this, for forging material 1, the form of the crystal grain in its m1 face and m3 face meets described formula (1) ~ (3).In contrast, m2 face is crystal grain 4 have bending form at long axis direction.So-called crystal grain 4 has bending form at long axis direction, and what refer to is not that picture forging extends material, and crystal grain is roughly formed as linearity at long axis direction, but as described later, the degree that when bending to welding, crackle can not be in progress along crystal grain boundary.At this, crystal grain 4 becomes the form bending to wavy (shape of crawling) on long axis direction.Further, in Fig. 2, be easy-to-understand to the form schematically showing crystal grain 4, in the tissues observed of reality, also meet the condition of described crystal grain 4.
Forging material 1 of the present invention, by the form making crystal grain 4 become such, the anti-thread breakage excellence of proper alignment.Its reason is as follows.
As shown in Figure 5, the crystal grain 4 of forging material 1 (three forging materials 3 direction forgings) has bending on long axis direction, forms being organized as the overlapping such form of lasagne of crystal grain 4.Relative to this, as shown in Figure 6, the crystal grain 40 of existing forging material 100 (two face forging materials (forging extends material) of 2 direction forgings) is linearly at long axis direction, forms being organized as the overlapping such form of bamboo of crystal grain 40.
At this, as shown in Figure 7,8, when forging the welding of material, because stress applies in the mode making crystal grain boundary tear, so crackle during welding is in progress along crystal grain boundary.In existing forging material, as shown in Figure 7, crystal grain is linearity on long axis direction, and therefore crackle is easily in progress along crystal grain boundary.In contrast, in forging material of the present invention, as shown in Figure 8, because crystal grain has bending (because crystal grain bends) at long axis direction, even if so when the part generation crackle of crystal grain boundary, crackle is also difficult to progress.That is, as shown in Figure 8, because crystal grain has bending at long axis direction, so the stress tearing crystal boundary diminishes relative to the stress be usually applied on crystal grain boundary.Thus, crackle is difficult to progress.Therefore, the anti-thread breakage excellence of proper alignment of forging material of the present invention.
Next, formula (1) ~ (3) are described.
Crystal grain is less, is more difficult to crackle occurs during welding, but if long-width ratio (major axis/minor axis) becomes large, then during welding, crackle easily carries out along major axis.Therefore about crystal grain diameter, the regulation of carrying out formula (1) ~ (3) is needed.It should be noted that, this formula (1) ~ (3) with test for according to derivation.
In formula (1), when GL is lower than 50 μm, proper alignment is anti-thread breakage, the anti-thread breakage reduction of anticorrosion stress-resistant.On the other hand, if higher than 500 μm, then anti-thread breakage, the anti-thread breakage reduction of anticorrosion stress-resistant of proper alignment.Therefore, be " 50 μm≤GL≤500 μm ".From the view point of improving further, proper alignment is anti-thread breakage, anticorrosion stress-resistant is anti-thread breakage, and GL is preferably less than 200 μm.
In formula (2), when GS is lower than 10 μm, proper alignment is anti-thread breakage, the anti-thread breakage reduction of anticorrosion stress-resistant.On the other hand, if higher than 180 μm, then anti-thread breakage, the anti-thread breakage reduction of anticorrosion stress-resistant of proper alignment.Therefore, be " 10 μm≤GS≤180 μm ".From the view point of improving further, proper alignment is anti-thread breakage, anticorrosion stress-resistant is anti-thread breakage, and GS is preferably less than 50 μm.
In formula (3), " GS≤GL " specifies, can be that major axis is longer or also can be major axis and minor axis be equal length than minor axis in crystal grain.
Further, if coarse grains, then there is the situation that intensity reduces.
Next, for the measuring method of GL and GS of crystal grain, be described for m3 face.Fig. 9 is the amplification profile schematic diagram in the m3 face of the measuring method of GL and GS that crystal grain is described.For buck on probation to after becoming minute surface, use Barker (Japanese: バ mono-カ mono-) family name's liquid to make it that anodic oxidation occur, use the opticmicroscope with polarized light to observe.
Grain-size measures crystal grain length GL μm and the crystal grain length GS μm in m3 face respectively with section method.
In fig .9, straight line A1-A2 is drawn along on long axis direction (transverse direction), measure the quantity (being 5 in this figure) of the crystal boundary of A1-A2 straight line crosscut thus, try to achieve GL (μm) by the length (μm) of the transverse direction with Fig. 9 divided by the quantity of (Japanese: cut り and return The) crystal boundary.
Equally, straight line B1-B2 is drawn along short-axis direction (longitudinal direction), measure the quantity (being 22 in this figure) of the crystal boundary of B1-B2 straight line crosscut thus, try to achieve GS (μm) by the length (μm) of the longitudinal direction with Fig. 9 divided by the quantity of crystal boundary.
In forging material, in order to be in the scope meeting formula (1) ~ (3), need to use aftermentioned specific manufacturing condition to manufacture.In addition as described later, in forging process, being carried out the forging of three by the mode reaching regulation with the forging ratio of each of ingot casting, can be the shape of regulation by the morphology Control of the crystal grain of forging material.
Then, the aluminium alloy forming forging material of the present invention is described.
Do not limit as the aluminium alloy for aluminum alloy forged material of the present invention, be preferably 7000 aluminium alloys being, particularly preferred consist of following.
(aluminium alloy)
Form the aluminium alloy of forging material preferably containing Mg:0.4 ~ 4.0 quality %, Zn:3.5 ~ 7.0 quality %, Cu:0.1 ~ 0.5 quality %, Mn: higher than 0.3 quality % and be below 0.8 quality %, Ti:0.001 ~ 0.15 quality %, in addition, also containing among Cr:0.1 ~ 0.5 quality %, Zr:0.05 ~ 0.25 quality % more than one, Si: be limited in below 0.5 quality %, Fe: be limited in below 0.5 quality %, and surplus is made up of Al and inevitable impurity.
Below, the content for each element forming aluminium alloy is described.
(Mg:0.4 ~ 4.0 quality %)
Mg has the effect that the tensile strength of aluminium alloy is improved.If the content of Mg is more than 0.4 quality %, then this effect becomes large.On the other hand, if the content of Mg is at below 4.0 quality %, then anticorrosion stress-resistant anti-thread breakage (SCC resistance) improves.Therefore, the content of Mg is preferably 0.4 ~ 4.0 quality %.From putting forward high-tensile viewpoint further, the content of Mg is more preferably more than 1.0 quality %, more preferably more than 1.5 quality %.In addition, anti-thread breakage from the view point of improving anticorrosion stress-resistant further, be more preferably below 2.5 quality %, more preferably below 2.0 quality %.
(Zn:3.5 ~ 7.0 quality %)
Zn has the effect that the tensile strength of aluminium alloy is improved.If the content of Zn is at more than 3.5 quality %, then this effect becomes large.On the other hand, if the content of Zn is at below 7.0 quality %, then anticorrosion stress-resistant anti-thread breakage (SCC resistance) improves.Therefore, the content of Zn is preferably 3.5 ~ 7.0 quality %.From putting forward high-tensile viewpoint further, the content of Zn is more preferably more than 4.0 quality %, more preferably more than 4.5 quality %.In addition, anti-thread breakage from the view point of improving anticorrosion stress-resistant further, be more preferably below 5.5 quality %, more preferably below 5.0 quality %.
(Cu:0.1 ~ 0.5 quality %)
Cu makes the erosion resistance of aluminium alloy reduce, but has the effect that anticorrosion stress-resistant anti-thread breakage (SCC resistance) and tensile strength are improved.If the content of Cu is at more than 0.1 quality %, then this effect becomes large.On the other hand, if the content of Cu is at below 0.5 quality %, then the anti-thread breakage raising of proper alignment.Therefore, the content of Cu is preferably 0.1 ~ 0.5 quality %.Anti-thread breakage and the tensile strength from the view point of further raising anticorrosion stress-resistant, the content of Cu is more preferably more than 0.15 quality %, more preferably more than 0.2 quality %.In addition, anti-thread breakage from the view point of improving proper alignment further, be more preferably below 0.3 quality %, more preferably below 0.25 quality %.
(Mn: higher than 0.3 quality % and be below 0.8 quality %)
Mn has the effect making crystal grain miniaturization.If the content of Mn is greater than 0.3 quality %, then this effect becomes large.On the other hand, if the content of Mn is at below 0.8 quality %, then thick intermetallic compound is difficult to produce, and therefore toughness improves, and during welding, crackle is difficult to progress.Therefore, the content of Mn is preferably higher than 0.3 quality % and is below 0.8 quality %.From the view point of increasing the effect making crystal structure miniaturization further, the content of Mn is more preferably more than 0.4 quality %.In addition, from the view point of improving toughness further, below 0.6 quality % is more preferably.
(Ti:0.001 ~ 0.15 quality %)
Ti has the effect of the crystal grain miniaturization after making casting.If the content of Ti is more than 0.001 quality %, then this effect becomes large.On the other hand, if the content of Ti is at below 0.15 quality %, then thick intermetallic compound is difficult to generate, and therefore toughness improves, and during welding, crackle is difficult to progress.Further, if the content of Ti is higher than 0.15 quality %, then its effect is saturated.Therefore, the content of Ti is preferably 0.001 ~ 0.15 quality %.From the view point of increasing the effect making crystal grain miniaturization further, the content of Ti is more preferably more than 0.005 quality %, more preferably more than 0.01 quality %.In addition, from the view point of improving toughness further, below 0.05 quality % is more preferably.
(Cr:0.1 ~ 0.5 quality %)
Cr, in casting process and heat treatment step, separates out as fine compound, has the effect suppressing grain growing.If the content of Cr is at more than 0.1 quality %, then this effect becomes large.On the other hand, if the content of Cr is at below 0.5 quality %, then thick as primary crystal Al-Cr series intermetallic compound is difficult to generate, and therefore toughness improves, and during welding, crackle is difficult to progress.Therefore, the content of Cr is preferably 0.1 ~ 0.5 quality %.From increasing this viewpoint of effect suppressing grain growing further, the content of Cr is more preferably more than 0.15 quality %.In addition, from the view point of improving toughness further, below 0.3 quality % is more preferably, more preferably below 0.25 quality %.
(Zr:0.05 ~ 0.25 quality %)
Zr has the crystal grain miniaturization making aluminium alloy, and makes the effect of its stabilization.If the content of Zr is more than 0.05 quality %, then this effect becomes large.On the other hand, if the content of Zr is at below 0.25 quality %, then thick crystallisate is difficult to generate, and therefore toughness improves, and during welding, crackle is difficult to progress.Therefore, the content of Zr is preferably 0.05 ~ 0.25 quality %.Make crystal grain miniaturization and the effect making its stabilization from the view point of increasing further, the content of Zr is more preferably more than 0.07 quality %, more preferably more than 0.1 quality %.In addition, from the view point of improving toughness further, below 0.2 quality % is more preferably, more preferably below 0.15 quality %.
Welded construction parts aluminium alloy of the present invention also can contain these Cr and Zr under the level of inevitable impurity, but in order to make crystal grain miniaturization, add among Cr and Zr more than one time, preferably contain in the scope of above-mentioned regulation.
(below Si:0.5 quality %)
Si is mixed in aluminium alloy usually used as matrix metal impurity, in casting process etc., makes to produce Al-Fe-Si series intermetallic compound in ingot casting.If the content of Si is at below 0.5 quality %, then thick Al-Fe-Si series intermetallic compound is difficult to produce in ingot casting, and toughness improves, and during welding, crackle is difficult to progress.Therefore, the content of Si is preferably below 0.5 quality %.From the view point of improving toughness further, the content of Si is more preferably below 0.3 quality %.
(below Fe:0.5 quality %)
Fe is also mixed in aluminium alloy usually used as matrix metal impurity, in casting process etc., makes to produce Al-Fe series intermetallic compound in ingot casting.If the content of Fe is at below 0.5 quality %, then thick Al-Fe series intermetallic compound is difficult to produce in ingot casting, and toughness improves, and during welding, crackle is difficult to progress.Therefore, the content of Fe is preferably below 0.5 quality %.From the view point of improving toughness further, the content of Fe is more preferably below 0.3 quality %.
(inevitable impurity)
As inevitable impurity, elements such as having B, C, Hf, Na can be imagined, no matter which kind of element, all allow to contain under the level not hindering feature of the present invention.Specifically, these inevitable impurity elements, the content of each element is preferably below 0.05 quality % respectively.In addition, the content of total is preferably below 0.15 quality %.
(manufacture method of aluminum alloy forged material)
Next, the welded construction parts embodiment of the manufacture method of aluminum alloy forged material of the present invention is described.
Welded construction parts of the present invention are the manufacture method of welded construction parts with aluminum alloy forged material of above-mentioned record by the manufacture method of aluminum alloy forged material, wherein, casting process, the heat treatment step that homogenizes, heating process, forging process and modified operation is carried out in order.
Below, each operation is described.It should be noted that, in the manufacture method of aluminum alloy forged material of the present invention, for casting process, the heat treatment step that homogenizes, heating process, can manufacture according to conventional methods, therefore these operations briefly be described.
(casting process)
Casting process is the operation of the ingot casting of cast aluminium alloy.As aluminium alloy, include, for example the aluminium alloy of the composition of above-mentioned record.In casting process, be suitable for selecting the common melt casting such as semicontinuous casting method (DC casting), heat top casting to cast.Further, after casting, also can utilize cutting machine etc., make ingot casting become the shape of expectation.
(homogenize heat treatment step)
The heat treatment step that homogenizes to homogenize heat treated operation to described ingot casting.The thermal treatment temp that homogenizes does not have special stipulation, but is 400 ~ 500 DEG C as an example.
(heating process)
Heating process is by the operation of the ingot casting heating after the described thermal treatment that homogenizes.By heating process, ingot casting is heated to forging and starts temperature.Heating temperature does not have special stipulation, but is 400 ~ 470 DEG C as an example.
(forging process)
Forging process forges the ingot casting after described heating with 350 ~ 460 DEG C and becomes the operation of forging material.In addition, forging process is the operation of the forging material being obtained the regulation shape as target by ingot casting.The forging of manufacture method of the present invention as described later, carries out three forgings.
Forging is roughly divided into open die forging and mould forging.And then in open die forging, be divided into the forging of only forging two faces to extend three forging materials of material and forging three.In open die forging, from the view point of productivity, use forges extension material more, but the major axis that forging extends the crystal grain of material becomes greatly, and the problem of large crackle easily occurs during existence welding.Confirm in the present invention, forged in the tissue formed by three forgings, mould, crystal grain has bending tissue at long axis direction, makes welding crack be difficult to occur.This is because as mentioned above, the stress being applied to crystal boundary when welding is disperseed, and crackle is difficult to progress.
It is 350 ~ 460 DEG C that forging starts temperature.When forging starts temperature lower than 350 DEG C, coarse grains, intensity, proper alignment are anti-thread breakage, the anti-thread breakage reduction of anticorrosion stress-resistant.On the other hand, if higher than 460 DEG C, then easily there is burning.Therefore, forging starts temperature is 350 ~ 460 DEG C.Be preferably 380 ~ 430 DEG C.
In order to reduce the strength that machining needs, the coarse grains preventing the crackle of former material, prevent because recrystallize during solution treatment causes, between forging end temp preferred administration to 180 ~ 450 DEG C.If forging end temp is more than 180 DEG C, then not only operating force quantitative change is low, and the burden of processor diminishes, and former material self is also difficult to crackle occurs.In addition, because processing strain reduces, therefore during solution treatment, crystal grain is difficult to coarsening.On the other hand, if forging end temp is below 450 DEG C, then as the intermetallic compound (Zn of low melting component
2mg etc.) problem (burning) of melting is difficult to occur.
When material temperature reduces in conducting forging processing, also suitably can return heating process, heat once again.
Forging process carries out following three forging process of more than 1 time, namely the ingot casting before forging is rectangular parallelepiped, if upper surface is A face, a side is B face, when a side adjacent with B face is C face, make the forging ratio of each be greater than 1.0S and for below 3.5S, carry out the forging in the forging in B face and C face, the forging in A face and C face, A face and B face so in order.
At this, so-called forging ratio represents the inverse of " section area before the section area/forging after forging ", i.e. " section area after the section area/forging before forging ", such as, about the area in A face, the area after expression forging becomes several times of the area before forging.Such as, if the area in A face after forging is " 1/2 " (0.5 times) of the area in A face before forging, then the forging ratio in A face is 2S.
Then, for the forging (three forgings) of this forging process, be described with reference to Figure 10.
As shown in Figure 10, the ingot casting before forging is rectangular parallelepiped.Shape as rectangular parallelepiped does not have special stipulation, can be cubes yet.Ingot casting is rectangular parallelepiped when forging, and except except becoming rectangular parallelepiped when the ingot casting of cast aluminium alloy, also in the front and back of each operation, can become rectangular parallelepiped by cutting etc.
The ingot casting of this rectangular parallelepiped has A face, the B face vertical with this A face and the C face vertical with B face with this A face.That is, ingot casting is setting A face as time above, is made up of A face, the face relative with this A face (below), side B, the face relative with this side B, C face, these 6, the face relative with this C face.
At this, when the forging ratio of each in A face, B face and C face is 2S, conveniently, be described for the rectangular parallelepiped of vertical 200mm × horizontal 370mm × long 400mm.But the size of rectangular parallelepiped does not have special stipulation.
In three forgings, first, the mode being 2S with the forging ratio in the A face of this rectangular parallelepiped forges B face and C face.Thus, become the rectangular parallelepiped of vertical 400mm × horizontal 296mm × long 250mm, the forging ratio in A face is 2S.That is, " forging ratio (S)=(400 × 370)/(250 × 296)=2 ".
Secondly, the mode being 2S with the forging ratio in the B face of this rectangular parallelepiped forges A face and C face.Thus, become the rectangular parallelepiped of vertical 250mm × horizontal 592mm × long 200mm, the forging ratio in B face is 2S.That is, " forging ratio (S)=(400 × 250)/(250 × 200)=2 ".
Then, the mode being 2S with the forging ratio in the C face of this rectangular parallelepiped forges A face and B face.Thus, become the rectangular parallelepiped of vertical 200mm × horizontal 370mm × long 400mm, the forging ratio in C face is 2S.That is, " forging ratio (S)=(250 × 592)/(200 × 370)=2 ".
Further, in described 3 forgings, if forging ratio is 2S, the size of the forging material before and after forging does not then have special stipulation.Such as, by the forging in described C face, if become the rectangular parallelepiped of vertical about 220mm × horizontal about 336mm × long 400mm, then " forging ratio (S)=(250 × 592)/(about 220 × about 336)=2 ".
These three forgings described above can carry out 1 time, also three forgings can be carried out more than 1 time or 2 times again.The upper limit does not have special stipulation, and the size according to the forging material expected determines.
In three forgings, in fact, be greater than 1.0S with the forging ratio of each and carry out with under type for 3.5S.If forging ratio is greater than 3.5S, then degree of finish is too high, likely because recrystallize causes organizing coarsening.In addition, be difficult to become crystal grain 4 and have bending form at long axis direction.In addition, forging former material becomes long bar-shaped, during the lower one side of forging, forges former material likely bending (flexing).Further, in order to carry out forging processing, the forging ratio of each is greater than 1.0S.Therefore, the forging ratio of each is for being greater than 1.0S and for below 3.5S.The viewpoint that the position never becoming forging tissue is difficult to remain is set out, and forging ratio is preferably more than 1.5S, is more preferably more than 2.0S.In addition, from making degree of finish more appropriate, in addition, forge former material and be difficult to become long bar-shaped viewpoint and set out, forging ratio is preferably below 3.0S, is more preferably below 2.0S.
Further, in the forging of each (3 times forging), if forging ratio is greater than 1.0S and is the scope of below 3.5S, then respective forging ratio can identical (being all such as 2S), and respective forging ratio also can be different.
Then, be greater than 1.0S with the forging ratio of each and carry out three forgings for the mode of below 3.5S, thus becoming crystal grain 4 at long axis direction and have bending form, and meeting formula (1) ~ (3).
(modified operation)
Modified operation is the operation of described forging material being carried out to T6 process or T7 process.
So-called T6 process is exactly the meaning of each process summarizing solution treatment, quenching, natural aging treatment, artificial aging process, carries out in this order.That is, the operation (T6 treatment process) that what is called carries out T6 process is meant to summarize the operation of each operation of solution treatment operation, quenching process, natural aging treatment operation, artificial aging treatment process, and each operation is carried out in this order.
So-called T7 process is exactly the meaning of each process summarizing solution treatment, quenching, natural aging treatment, stabilization treatment, carries out in this order.That is, the operation (T7 treatment process) that what is called carries out T7 process is meant to summarize the operation of each operation of solution treatment operation, quenching process, natural aging treatment operation, stabilization treatment operation, and each operation is carried out in this order.
(solution treatment operation)
Solution treatment operation is to reduce the operation of processing the strain that causes and making for the purpose of solute element solid solution.
Such as, between solid solution temperature preferred administration to 400 ~ 480 DEG C.If solid solution temperature is more than 400 DEG C, then solid solution is fully carried out, therefore, it is possible to show high-tensile.In addition, because the miniaturization of crystallisate is also easily carried out, so toughness is also difficult to reduce.On the other hand, if solid solution temperature is below 480 DEG C, then as the intermetallic compound (Zn of low melting component
2mg etc.) problem of melting can not occur.
Further, after solution treatment, also can carry out quench treatment by quenching process.Quench treatment is undertaken by cooling in water, in warm water.
(natural aging treatment operation)
Natural aging treatment operation puies forward high-tensile operation by causing precipitation from supersaturated solid solution.
Natural aging treatment preferably carries out more than 96 hours with normal temperature.Natural aging treatment is to make, for the purpose of the precipitation of fine and highdensity precipitate, to separate out to high-density, more can obtain high-tensile.But because be low temperature, speed of separating out is slow.When carrying out the process of more than 96 hours under normal temperature, these effects improve further.
In addition, if natural aging treatment is suitable, then not only intensity improves, and erosion resistance also improves.Further, if lack time effect (Japanese: Ami Time is imitated), then anticorrosion stress-resistant anti-thread breakage (SCC resistance) reduces, and in addition, welding crack easily occurs.
(artificial aging treatment process)
Artificial aging treatment process is that the precipitate of the forging material after natural aging treatment is grown, and increases the operation of tensile strength further.
Artificial aging process preferably carries out 5 ~ 48 hours with 90 ~ 180 DEG C.If artificial aging treatment temp is more than 90 DEG C, then the precipitate of natural aging treatment can fully grow, and can contribute to tensile strength and improve.On the other hand, if artificial aging treatment temp is below 180 DEG C, then a part for the precipitate of natural aging treatment can not solid solution again, and reaches high-tensile.In addition, the artificial aging treatment time is reached the conditional decision of the highest (peak value timeliness) by tensile strength under said temperature.If the artificial aging treatment time is more than 5 hours, then fully can be heated to forging material inner, not worry reducing in forging material inner tensile intensity.On the other hand, if within 48 hours, be then difficult to the effect condition that obsolesces, precipitate is difficult to become thick, can contribute to tensile strength and improve.
In addition, if artificial aging process is suitable, then not only intensity improves, and erosion resistance also improves.Further, if lack time effect, then welding crack easily occurs.
(stabilization treatment operation)
Stabilization treatment operation is that the precipitate of the forging material after natural aging treatment is grown, and makes the operation that tensile strength increases further.
Stabilization treatment is the overaging hardening treatment that the condition that exceedes the artificial age-hardening's treatment condition obtaining maximum strength is carried out.
Overaging hardening treatment preferably carries out 5 ~ 72 hours with 120 ~ 180 DEG C.If overaging hardening treatment temperature is more than 120 DEG C, then anticorrosion stress-resistant anti-thread breakage (SCC resistance) improves, and in addition, welding crack is difficult to occur.On the other hand, if overaging hardening treatment temperature is below 180 DEG C, then tensile strength improves.In addition, if the overaging hardening treatment time is more than 5 hours, then tensile strength improves.On the other hand, if the overaging hardening treatment time is within 72 hours, then anticorrosion stress-resistant anti-thread breakage (SCC resistance) improves, and in addition, welding crack is difficult to occur.
Welded construction parts of the present invention after carrying out artificial aging treatment process or stabilization treatment, can carry out the various welding processing such as electric-arc welding, plasma weldering, Laser Welding with aluminum alloy forged material.In addition, can carry out folding, cut, the various secondary processing such as surface treatment, change form, become actual goods.
Further, forging material of the present invention goes for the structure unit (welded construction parts) of the carrier vehicles such as automobile, motorcycle, rail truck, aircraft especially.
[embodiment]
Next, based on embodiment, the present invention is described.Further, the present invention is not by the restriction of embodiment shown below.
Use the Al alloy with composition shown in table 1, be cast as slab by DC casting.Thereafter keep this ingot casting 24hr with 450 DEG C and carry out homogenizing thermal treatment.Then, from this slab, cut the ingot casting block 50 of vertical 175mm × horizontal 360mm × long 150mm in the mode shown in Figure 11.
Thereafter, after the ingot casting block 50 cut is heated in the air furnace of 450 DEG C, use upper and lower mould, start temperature range with the forging shown in table 2,3 and carry out forge hot by oil press.
First forging is forging B face and C face and make A face be 2S.Secondly, forging A face and C face and make B face be 2S.Then, forge A face and B face and make C face be 2S.Thus, Al alloy forging material is as shown in Figure 1 manufactured.Wherein, for a part, forging plane number is 2.
In addition, use air furnace, keep Al alloy forging material 4hr with 460 DEG C and after carrying out solution treatment, quench with the water of 75 DEG C.Then, the Al alloy forging material quenched is carried out to the natural aging treatment of 120 hours with normal temperature.Thereafter, use air furnace, using as 120 DEG C of peak value timeliness, the condition of 24hr carries out artificial aging process.
Tension test test film is extracted and anticorrosion stress-resistant anti-thread breakage (SCC resistance) evaluation test film (C ring) from the Al alloy forging material so obtained.Use these test films, carry out the evaluation about tensile strength, SCC resistance.In addition, use the Al alloy forging material obtained to carry out welding test, evaluate for proper alignment is anti-thread breakage.Evaluation result is presented in table 2,3.In table 2,3, do not meet regulation of the present invention, logarithmic value is drawn underscore and is represented.
The characteristic evaluated in embodiment and comparative example is as follows.
[size of crystal grain]
For the Al alloy forging material manufactured, observe as shown in Figure 1 as m1, m2, m3 face of former material central part at position being formed with shear zone.Then, for m1 face, m3 face, according to the measuring method (section method) using Fig. 9 to illustrate, measure GL (major axis) and the GS (minor axis) of crystal grain.
Specific as follows.
For buck on probation to after becoming minute surface, use BarkerShi liquid to make it that anodic oxidation occur, use the opticmicroscope with polarized light to observe.
Grain-size, in m1 face and m3 face, measures crystal grain length GL μm and crystal grain length GS μm respectively with section method.Mean value respectively as n number=5 is tried to achieve.
In fig .9, straight line A1-A2 is drawn along long axis direction (transverse direction), measure by the quantity (being 5 in this figure) of the crystal boundary of this A1-A2 straight line crosscut, by the length (μm) of the transverse direction of Fig. 9 quantity divided by crystal boundary, thus try to achieve GL (μm).The mean value of 5 GL that obtains of method is as GL thus.
Equally, straight line B1-B2 is drawn along on short-axis direction (longitudinal direction), measure by the quantity (being 22 in this figure) of the crystal boundary of this B1-B2 straight line crosscut, by the length (μm) of the longitudinal direction of Fig. 9 quantity divided by crystal boundary, thus try to achieve GS (μm).The mean value of 5 GS that obtains of method is as GS thus.
About m2 face, grinding to after becoming minute surface for sample on probation, makes it that anodic oxidation occur with BarkerShi liquid, uses the form of the observation by light microscope crystal grain with polarized light.
Then, will meet
50≤GL≤500...(1)
10≤GS≤180...(2)
GS≤GL...(3)
Whole samples be judged to be qualified (zero).
[proper alignment is anti-thread breakage]
Anti-thread breakage about proper alignment, by carrying out welding test to evaluate.
First, from Al alloy forging material, extract the test film in A face, B face and C face.The test film in A face for front, indulges 100mm × horizontal 150mm × long 10mm with A face.The test film in B face and C face for front, is respectively vertical 50mm × horizontal 150mm × long 10mm with B face and C face.As shown in figure 12, the test film 7 of extraction is welded in welding material 8.
Welding material 8 uses 7N01 alloy as the aluminium alloy that can weld, and uses the sample being of a size of vertical (thickness) 35mm × horizontal 200mm × long 100mm.
As welding conditions, carry out the fillet welding of T word.Weld the mode to comprise the high position of degree of finish and the low position of degree of finish, carry out in the side (weld part) of the central part near Al alloy forging material.
Weldprocedure is that manual TIG welds (AC).The condition of manual TIG weldering uses DAIHEN society inverter elecon 500P, with polarity ratio: neutrality, welding current: 310A, arc voltage: 24V, welding speed: 4 ~ 17cm/min carry out.In addition, as shielding gas, flow through Ar gas with 15L/min.
The judgement of welding crack, is carried out with range estimation by dye check, if unconfirmed to crackle near weld part 9 in test film 7, is then judged to be qualified (zero).(do not judge to weld the crackle in material 8 and weld part 9.)
[tension test]
Tension test is No. 4 test films using JIS Z2201, according to the regulation of JIS Z2241, carries out the mensuration of tensile strength.For observed value, try to achieve as the mean value of the measured value of 30 test films in A face, B face, C face respectively.Tensile strength is when the material that 7000 are, qualified by being judged to be during more than 370MPa, other when, it is qualified to be judged to be by 240MPa.
[anticorrosion stress-resistant anti-thread breakage (SCC resistance)]
Stress corrosion cracking test uses the test film being attached with the stress of 300MPa, carries out 30 days with the salt solution alternating impregnating method of JIS H8711.At this moment, respectively for A face, B face, C face, 12 test films are tested, when all there is not stress corrosion cracking in whole test films, be judged to be qualified (zero).Further, the judgement of stress corrosion cracking, according to or without spread to C ring more than 1/2 be full of cracks carry out, chap lower than C ring 1/2 sample, the sample that do not have completely be qualified.
[table 1]
[table 2]
[table 3]
As Table 2,3, test material No.1 ~ 20 are because meet scope of the present invention, so whole assessment items is excellent.On the other hand, test material No.21 ~ 27 not meeting scope of the present invention are following result.It should be noted that, test material No.1 ~ 13 change material and the identical test material of forging condition, and test material No.14 ~ 27 are that material is identical and change the test material of forging condition.
No.21 is because forging starts temperature lower than lower value, so the GS in m3 face and m1 face is higher than higher limit, tensile strength, proper alignment are anti-thread breakage and SCC resistance is poor.
No.22 because the forging ratio of every one side is higher than the upper limit, so there is flexing during the forging of second.Therefore, mensuration and the evaluation of crystal grain is not carried out.
No.23 is because the forging ratio of every one side is higher than the upper limit, and in addition, forging plane number is 2, so crystal grain does not have bending, in addition, the GL in m3 face is higher than higher limit, and proper alignment is anti-thread breakage and SCC resistance is poor.
No.24 is because the forging ratio of every one side is higher than the upper limit, and in addition, forging plane number is 2, so crystal grain does not have bending, in addition, the GL in m3 face is higher than higher limit, and the GL in m1 face is lower than lower value, and proper alignment is anti-thread breakage and SCC resistance is poor.
No.25 is because forging plane number is 2, so crystal grain does not have bending, in addition, the GS in m3 face and m1 face is higher than higher limit, and tensile strength, proper alignment are anti-thread breakage and SCC resistance is poor.
No.26 is because forging starts temperature higher than higher limit, so generation burning.Therefore, mensuration and the evaluation of crystal grain is not carried out.
No.27 is because the forging ratio of every one side is higher than the upper limit, and in addition, forging plane number is 2, so crystal grain does not have bending, in addition, the GL in m3 face is higher than higher limit, GL and GS in m1 face is lower than lower value, and proper alignment is anti-thread breakage and SCC resistance is poor.
Nomenclature
The aluminum alloy forged material of 1 welded construction parts
4 crystal grain
7 test films
8 welding material (7N01 alloy)
The weld part that 9 manual TIG welding are formed
21 shear zones
22 dead-metal
50 ingot casting blocks
100 forgings extend material
Claims (3)
1. the aluminum alloy forged material of welded construction parts, it is characterized in that, in the tissue of described welded construction parts with aluminum alloy forged material, if the crystal grain length of major axis is GL μm, when the crystal grain length of minor axis is GS μm, among the face in mutually perpendicular 3 directions observed at the position being formed with shear zone, two faces are expressed from the next, its crystal grain of remaining one side has bending at long axis direction
50≤GL≤500...(1)
10≤GS≤180...(2)
GS≤GL...(3)。
2. the aluminum alloy forged material of welded construction parts according to claim 1, is characterized in that, the aluminum alloy forged material of described welded construction parts is made up of the aluminium alloy that 7000 are.
3. a welded construction parts manufacture method for aluminum alloy forged material, is characterized in that, is the manufacture method of the aluminum alloy forged material of welded construction parts according to claim 1 or claim 2, wherein, carries out following operation:
The casting process of the ingot casting of cast aluminium alloy;
The heat treated heat treatment step that homogenizes that homogenizes is carried out for described ingot casting;
The heating process of the ingot casting of heating after the described thermal treatment that homogenizes;
Forge the ingot casting after described heating with 350 ~ 460 DEG C and become the forging process of forging material;
Described forging material is carried out to the modified operation of T6 process or T7 process,
Described forging process carries out following three forging process of more than 1 time, namely the ingot casting before described forging is rectangular parallelepiped, if upper surface is A face, a side is B face, when a side adjacent with B face is C face, with the forging ratio of described each higher than 1.0S and be the mode of below 3.5S, carry out the forging in the forging in B face and C face, the forging in A face and C face, A face and B face in order.
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| JP2014066672A JP6185870B2 (en) | 2014-03-27 | 2014-03-27 | Aluminum alloy forging for welded structural member and method for producing the same |
| JP2014-066672 | 2014-03-27 |
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Cited By (2)
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|---|---|---|---|---|
| CN108971401A (en) * | 2018-09-25 | 2018-12-11 | 宁波锦越新材料有限公司 | A method of forging aluminum material |
| CN111996426A (en) * | 2020-08-30 | 2020-11-27 | 中南大学 | High-strength Al-Cu-Mg-Mn aluminum alloy and preparation method thereof |
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| JP2008150653A (en) * | 2006-12-15 | 2008-07-03 | Furukawa Sky Kk | Weldable aluminum alloy for forging having excellent stress corrosion cracking resistance, and forged part using the same |
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| CN102822376A (en) * | 2010-04-20 | 2012-12-12 | 美铝公司 | High strength forged aluminum alloy products |
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| JP3726034B2 (en) * | 2001-05-25 | 2005-12-14 | 株式会社神戸製鋼所 | Aluminum alloy welded joints and aluminum alloy sheet base materials for welded joints |
| US20030226935A1 (en) * | 2001-11-02 | 2003-12-11 | Garratt Matthew D. | Structural members having improved resistance to fatigue crack growth |
| JP5281031B2 (en) * | 2010-03-31 | 2013-09-04 | Ｊｘ日鉱日石金属株式会社 | Cu-Ni-Si alloy with excellent bending workability |
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| JP2002102983A (en) * | 2000-09-28 | 2002-04-09 | Aisin Seiki Co Ltd | Surface reforming method for light metal |
| JP2008150653A (en) * | 2006-12-15 | 2008-07-03 | Furukawa Sky Kk | Weldable aluminum alloy for forging having excellent stress corrosion cracking resistance, and forged part using the same |
| CN101688269A (en) * | 2007-05-14 | 2010-03-31 | 美铝公司 | Aluminum alloy products having improved property combinations and method for artificially aging same |
| CN102822376A (en) * | 2010-04-20 | 2012-12-12 | 美铝公司 | High strength forged aluminum alloy products |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN108971401A (en) * | 2018-09-25 | 2018-12-11 | 宁波锦越新材料有限公司 | A method of forging aluminum material |
| CN111996426A (en) * | 2020-08-30 | 2020-11-27 | 中南大学 | High-strength Al-Cu-Mg-Mn aluminum alloy and preparation method thereof |
| CN111996426B (en) * | 2020-08-30 | 2021-11-23 | 中南大学 | High-strength Al-Cu-Mg-Mn aluminum alloy and preparation method thereof |
Also Published As
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| JP6185870B2 (en) | 2017-08-23 |
| CN104946934B (en) | 2017-06-06 |
| JP2015188899A (en) | 2015-11-02 |
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