CN107532247A - high-strength aluminium alloy plate - Google Patents
high-strength aluminium alloy plate Download PDFInfo
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- CN107532247A CN107532247A CN201680024760.3A CN201680024760A CN107532247A CN 107532247 A CN107532247 A CN 107532247A CN 201680024760 A CN201680024760 A CN 201680024760A CN 107532247 A CN107532247 A CN 107532247A
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- Prior art keywords
- transition elements
- aluminium alloy
- dispersed granules
- plate
- intensity
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/05—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
Abstract
As being the tissue of the Al-Mg-Si-type aluminum alloy plate specifically formed containing transition elements, make average crystal grain diameter miniaturization, and nano level fine transition elements system dispersed granules be present, improved in conjunction with the intensity of processing hardenability band when being configured to structural elements, BH is improved, after room-temperature aging, is used as automotive structural members, also formability will not be hindered, and realizes the high intensity after BH.
Description
Technical field
The present invention relates to Al-Mg-Si-type aluminum alloy plate.Described aluminium alloy plate, refers to as hot rolled plate in the present invention
With the milled sheet of cold-reduced sheet etc., after quenched (T4) of solutionizing processing and Quenching Treatment etc. was implemented, it is configured to be made
Aluminium alloy plate before structural elements.In addition, in following description, aluminium is also referred to as aluminium and Al.
Background technology
In recent years, consider from earth environment etc., the light-weighted social desirability of the vehicle of automobile etc. grows to even greater heights.For
This requirement is tackled, as the material of automobile, in addition to the ferrous materials of steel plate etc., formability and coating baking hardening
(bake hardening ability, hereinafter also referred to BH) is excellent, and the application of the aluminium alloy material of more light weight increases.
The aluminium alloy plate of the larger panel timber-used of outer panels, wainscot as automobile etc., can typically illustrate Al-
The systems of the AA of Mg-Si systems to JIS 6000 (following, to be also only called 6000 systems) aluminium alloy plate.The 6000 line aluminium alloy plate, having must
Must the composition containing Si, Mg, formability is ensured with low yield strength (low-intensity) during shaping, the panel after shaping dries by application
Heating during artificial aging (hardening) processing of roasting processing etc., yield strength (intensity) improve, it can be ensured that the intensity of needs, i.e.,
Coating baking hardening is excellent.
In order that the further lightweight of car body, among automobile component, not only in the panel material, also it is desirable to
Expand aluminium in the skeleton material of vehicle frame, beam column etc., or the automotive structural members of armature such as bumper bar armature, door anti-collision joist etc.
The application of alloy material.
These automotive structural members are compared with the car panel, it is necessary to further high intensity.Therefore, in order to allow
6000 line aluminium alloy plate used in car panel material is stated, suitable for these skeleton materials or armature, it is necessary to further be allowed to high
Intensity.
But reach such high intensity, composition and manufacture without significantly changing existing 6000 line aluminium alloy plate
Condition, other characteristics such as formability and less easy are not hindered also.
All the time, as improve BH etc. so, as the panel material 6000 line aluminium alloy plates characteristic
And the organizational controls carried out, propose the various sizes of dispersed granules and the mode of number density for controlling transition elements systems.
For example, in patent document 1, as the panel material, proposition has a kind of 6000 line aluminium alloy plates, and it makes size
The mean number density of more than 0.5 μm of dispersed granules is 3000~20000/mm2, so that press formability and bending machining
Property improve.
The aluminium alloy plate, in embodiment, for plate after fabrication 3 months (after modifier treatment) during the room temperature of (90 days)
Plate after effect, after carrying out the artificial aging processing of 170 DEG C × 20 minutes after 2% strain imparting, 0.2% yield strength is high
It is only 205MPa or so intensity.
In addition, in patent document 2, as the panel material, proposition has a kind of press formability and crimping processability excellent
Different aluminium alloy plate, it is in order that the average crystal grain diameter miniaturization of recrystal grain to less than 45 μm, and makes dispersed granules
Average diameter is 0.02~0.8 μm, and makes mean number be 1/μm3More than.In the patent document 2, also for plate
Plate (after modifier treatment) after the room-temperature aging of 3 months (90 days) after fabrication, carry out deep-draw shaping after, then through 180 DEG C ×
After the artificial aging processing of 20 minutes, 0.2% yield strength height is only 205MPa or so intensity.
Prior art literature
Patent document
Patent document 1：Japanese Laid-Open 2007-169740 publications
Patent document 1：No. 3802695 publication of Japan's patent
In the control of the size of transition elements system dispersed granules in existing 6000 line aluminium alloy plate and a number density,
Also have a situation using the panel material as purposes, the intensity after artificial aging processing, in terms of 0.2% yield strength requirement have
More than 250MPa high intensity, in the purposes of the skeleton material or armature, intensity deficiency.
In contrast, even if by the artificial aging treatment temperature high temperature to such as 200 DEG C or so high intensity, people
0.2% yield strength after work Ageing Treatment can not still reach more than 250MPa high intensity.
Moreover, consider from intensity decreases etc. caused by treatment effeciency, funds, the deterioration of the coating toasted, overaging,
The temperature of artificial aging (hardening) processing can also have boundary and restriction certainly, also there is the situation for being unable to high temperature.
The content of the invention
The present invention does to solve such problem, it is intended that the structural elements as the automobile etc. is used, carries
For a kind of composition and manufacturing condition for not having to significantly change existing 6000 line aluminium alloy plate, high intensity just can be allowed to
6000 line aluminium alloy plates.
In order to reach this purpose, high-strength aluminium alloy plate of the invention will be intended to, a kind of Al-Mg-Si systems aluminium
Alloy sheets, it contains Mg respectively in terms of quality %：0.3~1.5%, Si：0.3~1.5%, and contain Mn：0.1~0.8%,
Zr：0.04~0.20%, Cr：0.04~0.20%, Sc：One or more among 0.02~0.1% are as transition member
Element, surplus are made up of Al and inevitable impurity, and as the tissue of the thickness of slab central part of the plate, average crystal grain diameter is 100 μ
Below m, and justified with the average equivalent of dispersed granules TEM-EDX measurements, containing the transition elements of 50,000 times of multiplying power
Diameter is in 50~300nm scope, also, diameter of equivalent circle is in the transition elements system dispersed granules of 20~400nm scope
Average number density is 5/μm3More than.
In the present invention, it is that aluminium closes for 6000 premised on not changing existing aluminium alloy composition, manufacturing condition significantly
Transition elements system dispersed granules in the tissue of golden plate influence to be studied again to caused by BH.
Its result is found, in the tissue of 6000 line aluminium alloy plates, nano level fine transition elements system dispersed granules
In the presence of real mass (substantive number), improved outside BH personality.
This is because, the fine transition elements system dispersed granules, not only make the structural elements that former material plate shapes exist
The yield strength (intensity) based on heating improves when artificial aging (hardening) through coating baking processing etc. is handled, and makes it
Processing hardening when former material plate to be configured to structural elements of leading portion improves.
That is, described fine transition elements system dispersed granules, there is following special effect, i.e. using former material plate into
Structural elements after the raising of processing hardening (intensity) during shape, and shaping handles the yield strength brought by artificial aging
The synergy that (intensity) improves, improve BH.
Moreover, the fine transition elements system dispersed granules, will not hinder former material plate to be configured to the formability of structural elements.
Therefore, before the present invention is so that the average crystal grain diameter of the thickness of slab central part of 6000 line aluminium alloy plates tiny (small) is
Carry, the fine transition elements system dispersed granules real mass be present, provide its average equivalent circular diameter and average in the lump
Density, so as to as vehicle structure as skeleton material, armature for requiring to have higher intensity than existing panel timber-used way etc.
Component use, do not hinder formability and being capable of high intensity.
Embodiment
Hereinafter, the mode of the implementation for the present invention, is specifically illustrated to each important document.、
(chemical composition composition)
First, below for the present invention Al-Mg-Si systems (hereinafter also referred to as 6000 systems) aluminium alloy plate it is chemical into
It is grouped into and illustrates.In the present invention, used as the skeleton material or armature, do not change existing composition, manufacture significantly
Condition, and carry out high intensity.
For problem as meeting in terms of the composition, in the composition of 6000 line aluminium alloy plates, in terms of quality %, contain respectively
There is Mg：0.3~1.5%, Si：0.3~1.5%, and contain Mn：0.1~0.8%, Zr：0.04~0.20%, Cr：0.04~
0.20%th, Sc：One or more among 0.02~0.1% are as transition elements, and surplus is by Al and inevitably miscellaneous
Texture into.Further, the % of the content of each element represents the entirely quality % meaning.
Illustrate each element in above-mentioned 6000 line aluminium alloy below contains scope and meaning or allowance.
Mg：0.3~1.5%
Mg contributes to solution strengthening together with Si, and in the artificial aging processing of coating baking processing etc., formed with
Help the precipitation of intensity raising, play age hardening capability, be for obtaining as needed for the structural elements of automobile etc.
The necessary element of yield strength wanted.
When Mg contents are less than 0.3%, intensity deficiency.On the other hand, if Mg contents are higher than 1.5%, shear band during cold rolling
Easily formed, the reason for turning into crackle during rolling.Therefore, Mg contents are more than 0.3%, preferably more than 0.4%, and
Less than 1.5%, preferably less than 1.2% scope.
Si：0.3~1.5%
Si contributes to solution strengthening and in the artificial aging processing of coating baking processing etc. together with Mg, formed with
Help the precipitation of intensity raising, play age hardening capability, be for obtaining as needed for the structural elements of automobile etc.
The necessary element for the intensity (yield strength) wanted.
When Si contents are less than 0.3%, intensity deficiency.On the other hand, if Si contents are higher than 1.5%, thick change is formed
Compound, deteriorate ductility.Therefore, Si contents are more than 0.3%, preferably more than 0.7%, and below 1.5%, are preferably
Less than 1.4% scope.
Mn、Zr、Cr、Sc
Mn, Zr, Cr, Sc transition elements, it is the main member for forming transition elements system dispersed granules specified in the present invention
Element.It forms transition elements system dispersed granules, makes crystal grain miniaturization and put forward intensity in the stage and final plate of ingot bar
It is high.In addition, these transition elements system dispersed granules, such as given to this invention, if being allowed to miniaturization to nanoscale, can also make
In the leading portion of artificial aging processing, processing hardening when former material plate to be configured to structural elements improves, with the structure after shaping
The raising of artificial age-hardening's ability (BH) of component is combined, and significantly improves the intensity after BH.
If Mn, Zr, Cr, Sc content are very few, the number densitys of the dispersed granules reduces, plate to structural elements shape when
Processing hardening and artificial age-hardening's ability (BH) reduce, the increase of the yield strength thereby resulted in reduces, described
Synergy diminishes, the level that the intensity after artificial aging processing can not increase to required by structural elements.
On the other hand, if Mn, Zr, Cr, Sc content are excessive, thick compound is easily formed, easily becomes destruction
Starting point, make ductility and strength deterioration on the contrary.
Therefore, containing Mn：0.1~0.8%, Zr：0.04~0.20%, Cr：0.04~0.20%, Sc：0.02~0.1%
Among one or more.
Other elements
In addition, in the present invention, in order that aluminium alloy plate high intensity, can also contain Cu：Less than 0.5% (but be free of
0%), Ag：0.01~0.2%, Sn：More than one or both of 0.001~0.1%.
Subsidiary one carries, because these elements have the effect for making plate high intensity jointly, is considered as the same of high intensity
Element, but its specific mechanism are imitated, has common part certainly, also there is different parts.
Cu improves intensity by solution strengthening etc..Ag for improve artificial age-hardening's ability (BH) it is useful, than
Under conditions of the artificial aging processing of low temperature, short time, there is the compound phase in the GP areas for promoting plate tissue etc. into crystal grain
The effect of precipitation.Sn has the effect that, captures atom vacancy, thus suppresses the diffusion of Mg and Si at room temperature, suppresses room temperature
Under intensity increase (room-temperature aging), when artificial aging handle, discharge the room of capture, promote Mg and Si diffusion, raising
BH.
But if the respective content of these elements is excessive, thick compound etc. is formed, the manufacture of plate is difficult, intensity
Reduced with bendability, in addition, corrosion resistance also reduces.If particularly Cu contents are excessive, bendability significantly reduces.
Therefore, these elements is contained sometimes, be the content below each higher limit.
Impurity
Other Fe, V, Ti, B, Zn etc., be it is easily mixed among waste material of melting raw material as ingot bar etc. can not
The impurity avoided, preferably few aspect, but also for the efficient activity of melting refinement, and it is allowed to what is allowed by JIS etc. specification
Content.For example, it is preferably less than 0.5% on Fe.
(tissue)
Be in 6000 as more than alloy chemical composition composition after, in the present invention, it is specified that this 6000 be aluminium close
The tissue of golden plate.That is, so that premised on the average crystal grain diameter of the thickness of slab central part of the plate tiny (small), make described fine
Transition elements system dispersed granules real mass is present, and provides its average equivalent circular diameter and average number density together.
These organization prescribeds, formed and manufacturing condition with not changing existing aluminium alloy significantly, or reduce formability
Premised on, it is to realize the important and necessary means of high intensity for improving the BH of 6000 line aluminium alloy plates.
Average crystal grain diameter：
Make the average crystal grain diameter of thickness of slab central part tiny (small), turning into makes the fine transition elements system disperse grain
The effect of son is able to the precondition played.That is, the grain structure of thickness of slab central part is average crystal grain diameter below 100 μm
Fine grain structure when, the effect of the fine transition elements system dispersed granules starts to play.The crystalline substance of thickness of slab central part
Grain tissue, when being higher than 100 μm of thick grain structure for average crystal grain diameter, the fine transition elements system dispersed granules
Effect halve or reduce.It means that the miniaturization of crystal grain, it may be said that be to ensure fine transition elements system dispersed granules
The precondition that effect plays.
Described crystal grain diameter in the present invention, it is in the longitudinal section of the rolling direction of the plate (plate cut off along rolling direction
Section) in, the crystal grain diameter of the rolling direction of thickness of slab central part.The measurement of the average crystal grain diameter, it is to pass through rolling direction
Line-intercept method evaluated.That is, it is by from the plate quenched through T4 being configured to before structural elements, extracting the longitudinal section
Thickness of slab central part sample, to sample surface carry out mechanical lapping after, tetrafluoro boric acid:Water=5:In 400 solution, with voltage
30V, 20~30 DEG C of solution temperature, 60~90 seconds time carry out electrolytic etching.Then, by using 50 times of light of polarizer
Microscope is learned, because of the deviation of the material in view of plate for the arbitrary measurement position of thickness of slab central part, passes through 10 visuals field
The visual observation of (every 5,1 visual field, every 500 μm of 1 line length) is carried out.
Transition elements system dispersed granules：
Average crystal grain diameter more than is as premise, as the tissue of the thickness of slab central part of plate, with 50,000 times of multiplying power
TEM-EDX measurements, the average equivalent circular diameters of transition elements system dispersed granules are in 50~300nm scope, also, equivalent
Circular diameter is 5/μm in the average number density of the transition elements system dispersed granules of 20~400nm scope3More than.
In the tissue of 6000 line aluminium alloy plates of artificial aging before processing, make the average equivalent of transition elements system dispersed granules
Circular diameter is 50~300nm scope, also, has the fine transition elements of the diameter of equivalent circle of 20~400nm scope
It is that dispersed granules exist as much as possible, and/μm of density 5 that average out3(exist more) during the above, then carried outside BH personality
It is high.
Although the mechanism that these transition elements system dispersed granules improve BH is still not clear, but be speculated as prestrain imparting
When Work Hardening Characteristic raising, due to assign prestrain and the dislocation that imports for the heat equivalent to baking application processing at
Recovery during reason suppresses, and the transition elements system dispersed granules of the size and number density are especially helpful.It is moreover, such micro-
Thin transition elements system dispersed granules, also there is the so excellent effect of the formability that former material plate will not be hindered to be configured to structural elements
Fruit.
The transition elements system dispersed granules with average equivalent circular diameter, or the diameter of equivalent circle with the scope
Transition elements system dispersed granules, heating when not only being handled via artificial aging make yield strength (intensity) improve, and
Make the former material plate of its leading portion to automotive structural members shape when processing hardening improve.Thus, the fine transition elements
Be dispersed granules, by former material plate to automotive structural members shape when the indurative raising of processing, and shaping after automobile knot
The synergy of the raising of artificial age-hardening's ability of structure component, and significantly improve BH.
Otherwise either the average equivalent circular diameter of transition elements system dispersed granules is as low as less than 50nm, in addition, coarsening
And it is higher than 300nm, the synergy that the intensity after the BH improves all can not be played or diminished.
In addition, the fine transition elements system dispersed granules of the diameter of equivalent circle of the scope with 20~400nm are averaged
Number density is less than 5/μm3When, the number of the fine transition elements system dispersed granules is very few, and the synergy can not be sent out
Wave.In the present invention, no matter large or small (diameter of equivalent circle), do not provide what can be measured by the TEM-EDX of described 50,000 times of multiplying power
The average number density of transition elements system dispersed granules.
Further, if from the boundary of manufacture, the fine mistake of the diameter of equivalent circle of the scope with the 20~400nm
The upper limit for crossing the average number density of first prime system dispersed granules is 100/μm3Left and right.
Why the average number density of so fine transition elements system dispersed granules tails off, and reason is first for the transition formed
Cellulose content deficiency.But in addition, even if form transition elements content content it is appropriate, due to plate preparation method the problem of,
Also having the transition elements system dispersed granules of generation can not grow, diameter of equivalent circle too small (meticulous) without 20nm, or vice versa
Excessively coarsening and the possibility higher than 400nm etc..
The measurement of transition elements system dispersed granules：
The fine transition elements system of the diameter of equivalent circle of the scope with 20~400nm specified in the present invention is more
The sub average number density of shot (individual/μm3), it is used to identify that (energy dispersion type X is penetrated by the EDX of (identification) dispersed granules by possessing
Line optical spectroscopy) function 50,000 times of multiplying power TEM (transmission electron microscopes：FE-TEM) measure.
It is the milled sheet of hot rolled plate and cold-reduced sheet etc. as the plate of measurement object, was implementing solutionizing processing and quenching
Processing etc. it is quenched after (T4 materials), processing hardening also turns into problem, therefore adds to be shaped for process bending machining etc.
Work is the aluminium alloy plate before used structural elements.
Specific measuring method, it is the sample that thickness of slab central part is extracted from the T4 materials before the shaping, TEM is being made
After film sample, the macrograph of thickness of slab central part is shot by the TEM of 50,000 times of multiplying powers, image procossing is carried out to it,
For (total area of field of view is 4 μm in the measurement visual field2More than) the measurable with diameter of equivalent circle of (identification) can be identified
The diameter of equivalent circle of transition elements system dispersed granules carry out whole measurements respectively.
Then, the average equivalent circular diameter of transition elements system dispersed granules is measured, and measures the model with 20~400nm
The transition elements system dispersed granules of the diameter of equivalent circle enclosed average number density (it is individual/μm3)。
Here, in the measurement of the average equivalent circular diameter and average number density, for being carried from arbitrary thickness of slab central part
10 samples taking are carried out, being averaged, as the scope with 20~400nm diameter of equivalent circle transition elements system more
The sub average number density of shot (individual/μm3)。
Described transition elements system dispersed granules, are the visuals field for the thickness of slab central part by tem observation in the present invention, are used
X-ray spectrometry device (EDX) is analyzed, and is identified accordingly containing transition more than one or both of Mn, Cr, Zr, Sc
First prime system dispersed granules (precipitate), identify other precipitates (dispersed granules) without these transition elements.Carry out this knowledge
When other, containing amount more than one or both of Mn, Cr, Zr, Sc, as long as the amount that can be detected by the EDX is (micro-
Amount), if in precipitate out of described the visual field, by the EDX be capable of detecting when one kind in Mn, Cr, Zr, Sc or
It is two or more, all it is transition elements system dispersed granules described in the present invention no matter then its amount.
Here, so-called diameter of equivalent circle, is exactly using the EDX, identifying (can identify), it is containing Mn, Cr, Zr, Sc
One or both of more than transition elements system dispersed granules, to this dispersed granules carry out image procossing, calculate the TEM and regard
The area of each transition elements system dispersed granules in open country, being converted into the diameter of bowlder of the same area, (circle of equal value is straight
Footpath) (circle equivalent diameter).
(manufacture method)
Then, illustrated below for the manufacture method of aluminium alloy plate of the present invention.Aluminium alloy plate of the present invention, manufacturing process
Itself it is conventional method or known method, after the aluminium alloy ingot bar of above-mentioned 6000 set member composition is cast, is homogenized
Heat treatment, and implement hot rolling, cold rolling and as defined thickness of slab, then implement the modifier treatment of solutionizing Quenching Treatment etc. and make
Make.
But in these manufacturing processes, in order to obtain present invention provide that tissue (transition elements system dispersed granules it is flat
The equal crystal grain diameter of equal number density peace), as be described hereinafter, to take preferable manufacturing condition.
(fusing, casting cooling speed)
First, in fusing, casting process, adjusted for fusing to the melting Al in above-mentioned 6000 set member compositing range
Alloy, suitably the common melting and casting method of continuously casting rolling, semi-continuous casting method (DC castings) etc. is selected to be cast
Make.
(homogenize heat treatment)
Secondly, for the aluminium alloy ingot bar cast, before hot rolling, the heat treatment that homogenizes is implemented.This homogenizes
It is heat-treated (all heat-treated), except general object, i.e. tissue homogenizes and (eliminates the segregation in the crystal grain in ingot bar tissue)
In addition, it is important that the dispersed granules miniaturization of transition elements system in other words, is exactly avoided its coarsening to nanoscale.
Therefore, equal heat condition can be an all heat-treated or secondary soaking or two sections of soaking, but its heating,
Cooling procedure needs to control.
So-called secondary soaking, it is exactly less than 200 DEG C of the temperature being first cooled to including room temperature after first time soaking
Degree, then reheated, after maintaining certain time with this temperature, start hot rolling.In contrast, so-called two sections of soaking, be exactly
Although being cooled down after first time soaking, less than 200 DEG C are not cooled to, but after higher temperature stops cooling, with this
After temperature maintains, directly start hot rolling with this temperature or after being again heated to higher temperature.
Soaking or the secondary first time hankered or two sections of equal heat conditions of the first paragraph hankered, be 500 DEG C with
Go up and be less than the temperature range of fusing point, in order to suppress the coarsening of transition elements system dispersed granules, controlled in defined chi
Under very little and number density, suitably selected from the scope of more than 1 minute and the retention time of less than 1 hour.
This soaking, or programming rate during the first paragraph soaking of the first time of secondary soaking or two sections of soaking is 100
DEG C/more than hr instant heating, in order that transition elements system dispersed granules nanoscale as fine to described as possible and separate out, preferably
Accelerate programming rate.Be less than 100 DEG C/hr if programming rate is slow, transition elements system dispersed granules coarsening has that can not use up can
Can the nanoscale and the possibility that separates out.
On the other hand, the cooling velocity after the first time soaking of secondary soaking, it is cold after the first paragraph soaking of two sections of soaking
But speed is 40 DEG C/below hr, preferably 30 DEG C/below hr, is not preferably let cool outside stove, but is let cool in stove, and normal
Rule method is on the contrary, make cooling velocity as small as possible (slow).
Thus, the precipitation and growth of the nano level fine transition elements system dispersed granules in cooling are promoted, will
It is controlled in defined size and number density.
In addition, in a soaking process, the cooling velocity after an all heat-treated is it is also preferred that as small as possible (slow), is
40 DEG C/below the hr.
Second or the equal heat condition of second segment, preferably more than hot rolling start temperature and less than 500 DEG C of temperature range,
The scope selection of the retention time of more than 30 minutes, reheats the ingot bar after first time soaking, cooling, is cooled to hot rolling and starts temperature
Degree, or hot rolling start temperature is again heated to, kept in this neighborhood.Alternatively, it is also possible to which the ingot bar after first paragraph soaking is cooled to
Hot rolling start temperature, kept in this neighborhood.This second or the soaking temperature of second segment, than first time or first paragraph soaking temperature
It is low.In addition, in once equal heat condition, to the time of hot rolling start temperature after control soaking, same effect can be also obtained.
In addition, on this second or the heating of soaking temperature of second segment, soaking after cooling velocity because described
First time or first paragraph soaking process in form the transition elements system dispersed granules of desired morphology, so if meet with
The category of lower described hot-rolled condition, then need not especially make programming rate and cooling velocity be in identical condition and range.
(hot rolling)
Homogenize heat treatment ingot bar hot rolling, according to the thickness of slab of rolling, by the roughing operation of ingot bar (slab)
Formed with finish to gauge process.In this roughing operation and finish to gauge process, suitably using the milling train of reversible or tandem etc..
As the start temperature of the hot roughing of hot rolling start temperature, in a soaking process be preferably more than 350 DEG C and
It it is preferably more than 350 DEG C and less than 400 DEG C in secondary soaking process below solidus temperature.The start temperature of hot roughing is low
When 350 DEG C, its hot rolling of any soaking process material is difficult, otherwise be higher than 400 DEG C, in secondary soaking process material, and transition
First thick precipitation of prime system dispersed granules, it is impossible to nanoscale as fine to described as possible and the possibility that separates out is high.In addition, on one
Secondary soaking process material, soaking time is set to carry out hot rolling immediately after the progress of defined time range, so as to suppress transition member
The coarsening of prime system dispersed granules, hot rolling is carried out in the state of the transition elements system dispersed granules for it is expected form are maintained.
After such hot roughing, hot finish to gauge of the end temp in 300~350 DEG C of scope is preferably carried out.The hot finish to gauge
End temp it is too low and during less than 300 DEG C, rolling loads are high, and productivity ratio reduces.On the other hand, for not a large amount of residual process
Organize and turn into recrystallized structure, when the end temp of hot finish to gauge is improved for this, if its temperature is higher than 350 DEG C, transition elements
It is the thick precipitation of dispersed granules, it is impossible to which the possibility for being allowed to nanoscale as fine to described as possible and separating out is high.
(annealing of hot rolled plate)
The hot rolled plate need not anneal (black annealing) before cold rolling, but can also implement.
(cold rolling)
In cold rolling, roll above-mentioned hot rolled plate, be fabricated to the cold-reduced sheet of desired final thickness of slab (also including coiled material).But
It is, in order that crystal grain more miniaturization, it is desirable to cold rolling rate is more than 30%, in addition for the purpose same with the black annealing,
Intermediate annealing can be carried out between cold rolling pass.
(solutionizing and Quenching Treatment)
After cold rolling, solutionizing processing is carried out, next proceeds to the Quenching Treatment of room temperature.At this solutionizing quenching
Reason, can use common continuous heat-treatment lines.But in order to obtain the sufficient solid solution capacity of Mg, Si etc. each element, preferably
After carrying out solutionizing processing at temperature more than 550 DEG C and below melting temperature, it is 20 to make to the average cooling rate of room temperature
More than DEG C/sec.At the temperature lower than 550 DEG C, the compound of Mg-Si systems of solutionizing before processing generation etc. is dissolved not again
Fully, being dissolved Mg amounts and solid solution Si amounts reduces.
In addition, when average cooling rate is less than 20 DEG C/sec, the precipitate of Mg-Si systems is mainly generated in cooling, is dissolved Mg
Amount and solid solution Si amounts reduce, it is impossible to ensure that the possibility of Si and Mg solid solution capacity is still high.In order to ensure the cooling velocity, quenching
Selection uses the air cooling of fan etc., the water cooling means and condition of spraying, spray, dipping etc. respectively for processing.
(Pre-aging treatment：Reheating processing)
After progress Quenching Treatment after such solutionizing is handled is cooled to room temperature, preferably to cold rolling within 1 hour
Plate carries out Pre-aging treatment (reheating processing).To room temperature Quenching Treatment terminate after, if starting to Pre-aging treatment, (heating is opened
Begin) room temperature i time it is long, then due to room-temperature aging, cause rich Si Mg-Si clusters to generate, it is difficult to make Mg's and Si
Balance good Mg-Si clusters increase.Therefore, the room temperature i time is more short better, solutionizing and Quenching Treatment and reheating
Processing, can also almost no time difference and be carried out continuously, the time of lower limit does not set especially.
The Pre-aging treatment, the retention time at 60~120 DEG C is preferably set to be carried out for more than 5 hours and less than 40 hours
Keep.Thus, the good Mg-Si clusters of Mg and Si balance can be formed.
If pre-age temperature be less than 60 DEG C, or the retention time be less than 10 hours, then with the situation without the Pre-aging treatment
Equally, it is difficult to suppress rich Si Mg-Si clusters, it is difficult to the Mg and Si is kept the Mg-Si clusters increase of balance, baking applies
The easy step-down of yield strength after dress.
On the other hand, preageing condition is higher than 120 DEG C, or more than 40 hours, it is excessive to separate out the growing amount of core, toasts application
Intensity during preceding bending machining becomes too high, and bendability easily deteriorates.
Hereinafter, enumerate embodiment and further illustrate the present invention, the present invention is not limited by following embodiments certainly, can
The scope of objective described later can also suitably be changed implementation before meeting, and these are all contained in the technical scope of the present invention
It is interior.
Embodiment
As embodiments of the invention, change composition and manufacturing condition, manufacture the nano level fine transition respectively
The average number densities of the first prime system dispersed granules 6000 line aluminium alloy plates different with average crystal grain diameter.Then, measure, evaluate plate
BH (coating baking hardening) after manufacture.Its result is shown in table 1,2,3.
The specific manufacture method respectively, it is directed to 6000 line aluminium alloy plates of the composition shown in table 1, such as the institute of table 2,3
Show, the manufacturing condition of equal heat condition and hot roughing start temperature etc. is carried out various changes.
Here, in the expression of the content of each element in table 1, what the numerical value of each element showed for blank, represent its content
Below detectable limit (0%).
The specific manufacturing condition of aluminium alloy plate is as follows.For the aluminium alloy ingot bar of each composition shown in table 1, commonly through
DC casting meltings.Next, for ingot bar, after each example carries out all heat-treated with each different condition shown in table 2,3,
Hot roughing is started with each different temperatures shown in table 2,3.
Then, each example is common, hot finish to gauge of the end temp in 300~350 DEG C of scope is carried out, all as thickness
4.0mm hot rolled plate.For hot rolled plate, each example without the intermediate annealing in the black annealing after hot rolling, and cold rolling pass way, and
The cold rolling of rate 50% is processed, the cold-reduced sheet as thickness 2.0mm.
Again for each cold-reduced sheet, with the condition of each example all same, modifier treatment (T4) is carried out with Equipment for Heating Processing.It is specific next
Say, solutionizing processing was carried out with 550 DEG C × 30 minutes, at this moment, the average heating rate to the solutionizing treatment temperature is 10
DEG C/sec, the water cooling that average cooling rate is 100 DEG C/sec is carried out after solutionizing processing, is cooled to room temperature.In addition, immediately this is cooled down
Afterwards, Pre-aging treatments are carried out with 100 DEG C of conditions kept for 8 hours immediately, slow cooling (letting cool) after Pre-aging treatment.
Cut on each end article plate after being placed 2 weeks with room temperature after these modifier treatment for test plate (panel) (blank), according to
The measuring method, measures the average equivalent circular diameter (nm) of each transition elements system dispersed granules for test plate (panel), and with 20~
The transition elements system dispersed granules of the diameter of equivalent circle of 400nm scope average number density (it is individual/μm3), average crystal grain diameter
The tissue of (μm) etc..
In addition, measure, evaluate each BH for test plate (panel).These results are shown in table 2,3.
(BH)
By tension test, 0.2% yield strength (the As yield strengths for respectively supplying test plate (panel) are tried to achieve respectively：T4 materials=into
The yield strength of plate before shape and BH), 0.2% yield strength after 2% stretching, through artificial age-hardening after 2% stretching
0.2% yield strength after processing (after BH).
Described 2% stretching, it is to simulate the stretching of bending machining to the shaping of structural elements as former material plate, when artificial
Imitate the condition that cure process (BH) is 185 DEG C × 20 minutes.
In table 2,3, the As0.2% yield strengths are sequentially shown, 0.2% yield strength after 2% stretching
Incrementss, 0.2% yield strength after the BH.
In the tension test, from it is described respectively on test plate (panel), extract respectively JIS Z 2201 No. 5 test films (25mm ×
50mmGL × thickness of slab), tension test is carried out at room temperature.It is parallel side to make the draw direction of test film at this moment and rolling direction
To.In addition, with gauge length 50mm, 5mm/ points of draw speed, carried out under certain speed until test film is broken.The characteristic of machinery
The N numbers of measurement are 5, respectively with mean value calculation.
As table 1,2 is respectively shown in, each example 1~13 is in the composition compositing range of the present invention, and in preferable bar
Part scope manufactures.Therefore, each example is as shown in table 2, has such as tissue (transition elements system dispersed granules given to this invention
Average equivalent circular diameter, diameter of equivalent circle be 20~400nm scope transition elements system dispersed granules average number density,
Average crystal grain diameter).
Its result understands that these each examples, after room-temperature aging, as shown in table 2,0.2% surrender after BH is strong
Degree is also high, is high intensity.That is, the incrementss of 0.2% yield strength after described 2% stretching are up to more than 33MPa, former material plate to
Processing hardening when automotive structural members shape improves.
And understand, carried by with the yield strength (intensity) during the processing of the artificial aging of the automotive structural members after shaping
High synergy, BH improve significantly to more than 262MPa.
In contrast, the comparative example 14~21 of table 3, uses the example identical alloy example 1,4 with table 1.But these
Each comparative example is as shown in table 3, and the manufacturing condition of equal heat condition, hot roughing start temperature etc. departs from preferable condition.
Its soaking temperature of comparative example 14 is too low and is less than 500 DEG C.
Programming rate during 15,18,21 its soaking of comparative example is excessively slow and is less than 100 DEG C/hr.
Cooling velocity after its soaking of comparative example 19 is too fast and is higher than 40 DEG C/hr.
Comparative example 15,16,18 is secondary soaking process, but hot roughing start temperature it is too high and more than 400 DEG C.
Comparative example 17,20 is secondary soaking process, but hot roughing start temperature it is too low and less than 350 DEG C.
Therefore, these comparative examples, its diameter of equivalent circle are the flat of the transition elements system dispersed granules of 20~400nm scope
Equal number density, average crystal grain diameter, depart from tissue given to this invention.
As a result, compared with the example formed as same alloy, 0.2% yield strength after 2% stretching
Even if incrementss it is high, also as little as 30MPa or so, the synergy improved with yield strength during BH cannot play, room temperature
It is also poor to 248MPa or so even if the BH after timeliness is high.
Although the comparative example 22~27 of table 3 manufactures in preferable condition and range, the alloy of table 1 has been used to form difference
Depart from the alloy numbering 9~14 of the scope of the invention.
Comparative example 22,23 is that Mn, Zr, Cr, Sc of the alloy numbering 9,10 of table 1 content are very few.
Comparative example 24 is the alloy numbering 11 of table 1, and Mg content is very few.
Comparative example 25 is the alloy numbering 12 of table 1, and Mg content is excessive.
Comparative example 26 is the alloy numbering 13 of table 1, and Si content is very few.
Comparative example 27 is the alloy numbering 14 of table 1, and Si content is excessive.
Therefore, these comparative examples are as shown in table 3, transition elements system disperse of the diameter of equivalent circle in 20~400nm scope
The average number density of particle, average crystal grain diameter etc., depart from from tissue given to this invention.
As a result, even if the incrementss of 0.2% yield strength after 2% stretching are high, also as little as 30MPa or so,
The synergy improved with yield strength during BH cannot play, also poor to 244MPa even if the BH after room-temperature aging is high
Left and right.
Therefore, it is embodiment as a result, it was confirmed that after room-temperature aging more than, for high intensity, also there is whole
Meet the necessity of composition and tissue given to this invention.
[table 1]
In detail and the present invention is illustrated with reference to specific embodiment, but do not depart from the spirit and scope of the present invention to add
With various changes and modifications, this will be apparent that for practitioner.
The application is based on Japanese patent application (patent application 2015-108596) filed in 28 days Mays in 2015, in it
Hold reference herein to be incorporated into.
Industrial applicability
In accordance with the invention it is possible to provide 6000 line aluminium alloy plates of high intensity.As a result, in addition to panel material,
6000 line aluminium alloy plates can also be as the reinforcement of the skeleton material or, bumper bar armature, door anti-collision joist etc. of vehicle frame, beam column etc.
The automotive structural members of material etc. and expand its application.
Claims (2)
1. a kind of high-strength aluminium alloy plate, it is characterised in that be following Al-Mg-Si-type aluminum alloy plate, it is in terms of quality %
Contain Mg respectively：0.3~1.5%, Si：0.3~1.5%, and contain Mn：0.1~0.8%, Zr：0.04~0.20%, Cr：
0.04~0.20%, Sc：For one or more among 0.02~0.1% as transition elements, surplus is by Al and can not keep away
The impurity exempted from is formed,
As the tissue of the thickness of slab central part of the plate, average crystal grain diameter is below 100 μm, and with 50,000 times of multiplying power
The average equivalent circular diameter of dispersed granules that TEM-EDX are measured, containing the transition elements is 50~300nm scope,
Also, diameter of equivalent circle is 5/μm in the average number density of the transition elements system dispersed granules of 20~400nm scope3With
On.
2. high-strength aluminium alloy plate according to claim 1, wherein, the aluminium alloy plate also contains Cu：Less than 0.5% but
Without 0%, Ag：0.01~0.2%, Sn：More than one or both of 0.001~0.1%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015108596A JP6810508B2 (en) | 2015-05-28 | 2015-05-28 | High-strength aluminum alloy plate |
| JP2015-108596 | 2015-05-28 | ||
| PCT/JP2016/065682 WO2016190409A1 (en) | 2015-05-28 | 2016-05-27 | High-strength aluminum alloy plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107532247A true CN107532247A (en) | 2018-01-02 |
| CN107532247B CN107532247B (en) | 2019-07-05 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201680024760.3A Expired - Fee Related CN107532247B (en) | 2015-05-28 | 2016-05-27 | High-strength aluminium alloy plate |
Country Status (4)
| Country | Link |
|---|---|
| US (1) | US20180363113A1 (en) |
| JP (1) | JP6810508B2 (en) |
| CN (1) | CN107532247B (en) |
| WO (1) | WO2016190409A1 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109468504A (en) * | 2018-11-21 | 2019-03-15 | 安徽鑫铂铝业股份有限公司 | A kind of corrosion-resistant automotive light weight technology aluminum profile |
Families Citing this family (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP6433380B2 (en) * | 2014-06-27 | 2018-12-05 | 株式会社神戸製鋼所 | Aluminum alloy rolled material |
| JP2018100435A (en) * | 2016-12-20 | 2018-06-28 | 株式会社神戸製鋼所 | Aluminum alloy sheet |
| CN106521258A (en) * | 2016-12-28 | 2017-03-22 | 南京理工大学 | High-strength silicon aluminum alloy and preparation method thereof |
| CN110662852A (en) * | 2017-05-26 | 2020-01-07 | 诺维尔里斯公司 | High strength corrosion resistant 6XXX series aluminum alloys and methods of making the same |
| EP3821048A1 (en) | 2018-09-24 | 2021-05-19 | Aleris Rolled Products Germany GmbH | Aluminium alloy fin stock material |
| CN113737064B (en) * | 2021-08-31 | 2022-04-08 | 华中科技大学 | Al-Mg-Si alloy for high-performance forge piece and preparation method thereof |
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| JP2000226629A (en) * | 1999-02-05 | 2000-08-15 | Kobe Steel Ltd | Al-Mg-Si ALUMINUM ALLOY SHEET FOR FORMING EXCELLENT IN SURFACE PROPERTY |
| JP2001294965A (en) * | 2000-04-12 | 2001-10-26 | Toyota Motor Corp | Aluminum alloy sheet excellent in crushability and method for producing part using the same |
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2015
- 2015-05-28 JP JP2015108596A patent/JP6810508B2/en active Active
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2016
- 2016-05-27 CN CN201680024760.3A patent/CN107532247B/en not_active Expired - Fee Related
- 2016-05-27 US US15/573,887 patent/US20180363113A1/en not_active Abandoned
- 2016-05-27 WO PCT/JP2016/065682 patent/WO2016190409A1/en active Application Filing
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| JPH04160131A (en) * | 1990-10-23 | 1992-06-03 | Kobe Steel Ltd | Al-mg-si alloy plate excellent in strength and formability, and its manufacture |
| JP2000226629A (en) * | 1999-02-05 | 2000-08-15 | Kobe Steel Ltd | Al-Mg-Si ALUMINUM ALLOY SHEET FOR FORMING EXCELLENT IN SURFACE PROPERTY |
| JP2001294965A (en) * | 2000-04-12 | 2001-10-26 | Toyota Motor Corp | Aluminum alloy sheet excellent in crushability and method for producing part using the same |
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2016190409A1 (en) | 2016-12-01 |
| JP2016222959A (en) | 2016-12-28 |
| CN107532247B (en) | 2019-07-05 |
| US20180363113A1 (en) | 2018-12-20 |
| JP6810508B2 (en) | 2021-01-06 |
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