CN107532247B - High-strength aluminium alloy plate - Google Patents
High-strength aluminium alloy plate Download PDFInfo
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- CN107532247B CN107532247B CN201680024760.3A CN201680024760A CN107532247B CN 107532247 B CN107532247 B CN 107532247B CN 201680024760 A CN201680024760 A CN 201680024760A CN 107532247 B CN107532247 B CN 107532247B
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- transition elements
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- aluminium alloy
- dispersed granules
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Classifications
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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
-
- 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 the tissue for containing transition elements being the Al-Mg-Si-type aluminum alloy plate specifically formed, it miniaturize average crystal grain diameter, and the transition elements system dispersed granules for keeping nanoscale fine exist, it is improved in conjunction with processing hardening bring intensity when being configured to structural elements, improve BH, even if using after room-temperature aging as automotive structural members, 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 plates.Described aluminium alloy plate, refers to as hot rolled plate in the present invention
It is configured to be made after quenched (T4) for implementing solutionizing processing and quenching treatment etc. with the milled sheet of cold-reduced sheet etc.
Aluminium alloy plate before structural elements.In addition, aluminium is also known as aluminium and Al in description below.
Background technique
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 coped with, as the material of automobile, other than the steel material 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 is increasing.
The aluminium alloy plate of the larger panel material of outer panels, inner panel as automobile etc., can typically illustrate Al-
6000 system of AA to JIS (hereinafter, being also only called 6000 systems) aluminium alloy plate of Mg-Si system.The 6000 line aluminium alloy plate, having must
Formability must be ensured with low yield strength (low-intensity) when forming, the panel after forming is dried by coating containing the composition of Si, Mg
Heating when 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 to make the further lightweight of car body, among automobile component, not only in the panel material, also it is desirable to
Expand aluminium in the automotive structural members of the armatures such as the skeleton material or bumper bar armature, door anti-collision joist of vehicle frame, beam column etc. etc.
The application of alloy material.
These automotive structural members need further high intensity compared with the car panel.Therefore, in order to allow
6000 line aluminium alloy plate used in car panel material is stated, these skeleton materials or armature are suitable for, needs further to be allowed to high
Intensity.
But reach such high intensity, composition and manufacture without substantially changing existing 6000 line aluminium alloy plate
Condition does not hinder other characteristics such as formability also and is less easy.
All the time, as improve BH etc. in this way, as the panel material 6000 line aluminium alloy plates characteristic
And the organizational controls carried out, propose the size of the dispersed granules of various control transition elements systems and the mode of number density.
For example, in patent document 1, as the panel material, proposition there are a kind of 6000 line aluminium alloy plates, make size
The mean number density of 0.5 μm or more 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) when the room temperature of (90 days)
Plate after effect, after carrying out artificial aging processing in 170 DEG C × 20 minutes after 2% strain imparting, 0.2% yield strength is high
It is only the intensity of 205MPa or so.
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, in order to miniaturize the average crystal grain diameter of recrystal grain to 45 μm hereinafter, and making dispersed granules
Average diameter is 0.02~0.8 μm, and makes 1/μm of mean number3More 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 forming after, then through 180 DEG C ×
After artificial aging processing in 20 minutes, 0.2% yield strength height is only the intensity of 205MPa or so.
Existing technical literature
Patent document
Patent document 1: Japanese Laid-Open 2007-169740 bulletin
Patent document 1: No. 3802695 bulletin of Japan's patent
In the control of the size and number density of the transition elements system dispersed granules in existing 6000 line aluminium alloy plate,
Also there is the case where using the panel material as purposes, artificial aging treated intensity, requirement has in terms of 0.2% yield strength
The high intensity of 250MPa or more, the skeleton material or armature use on the way, intensity is insufficient.
In contrast, even if by the artificial aging treatment temperature high temperature to such as 200 DEG C or so high intensity, people
The high intensity of working hour effect treated 0.2% yield strength cannot still reach 250MPa or more.
Moreover, strength reduction caused by treatment effeciency, funds, the deterioration of the coating of baking, the overaging etc. considers,
The case where temperature of artificial aging (hardening) processing can also have boundary and restriction certainly, also be unable to high temperature.
Summary of the invention
The present invention does to solve such project, it is intended that the structural elements as the automobile etc. is used, mentions
For a kind of composition and manufacturing condition without substantially changing 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 system aluminium
Alloy sheets, in terms of quality % respectively contain Mg:0.3~1.5%, Si:0.3~1.5%, and containing Mn:0.1~0.8%,
Zr:0.04~0.20%, Cr:0.04~0.20%, Sc:0.02~0.1% one or more of as transition member
Element, surplus are made of Al and inevitable impurity, the tissue of the plate thickness central part as the plate, and average crystal grain diameter is 100 μ
M is hereinafter, and with the TEM-EDX of 50,000 times of multiplying power measurement, dispersed granules containing transition elements average equivalent circle
Diameter is in the range of 50~300nm, also, equivalent circle diameter is in the transition elements system dispersed granules of the range of 20~400nm
Average number density is 5/μm3More than.
It in the present invention, is that aluminium closes for 6000 premised on not changing existing aluminium alloy composition, manufacturing condition substantially
Transition elements system dispersed granules in the tissue of golden plate influence to be studied again caused by BH.
Itself as a result, it has been found that, in the tissue of 6000 line aluminium alloy plates, the fine transition elements system dispersed granules of nanoscale
In the presence of real mass (substantive number), improved outside BH personality.
This is because, the fine transition elements system dispersed granules, the structural elements for not only shaping former material plate 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, the fine transition elements system dispersed granules, have the effect of following special, that is, using former material plate at
Structural elements after the raising of processing hardening (intensity) when shape, and forming handles bring yield strength by artificial aging
The synergy that (intensity) improves improves 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, the present invention so that the average crystal grain diameter of the plate thickness central part of 6000 line aluminium alloy plates it is tiny it is (small) be before
It mentions, there is the fine transition elements system dispersed granules real mass, provide its average equivalent circular diameter and average together
Density, thus as vehicle structure as skeleton material, armature for requiring to have higher intensity than existing panel material purposes etc.
Component use, do not hinder formability and being capable of high intensity.
Specific embodiment
Hereinafter, being specifically illustrated for the mode of implementation of the invention to each important document.,
(chemical component composition)
Firstly, below for Al-Mg-Si system (hereinafter also referred to as 6000 systems) aluminium alloy plate of the invention chemistry at
It is grouped as and is illustrated.In the present invention, it is used as the skeleton material or armature, does not change existing composition, manufacture substantially
Condition, and carry out high intensity.
In order in the composition of 6000 line aluminium alloy plates, in terms of quality %, contain respectively from project as composition aspect meets
Have Mg:0.3~1.5%, Si:0.3~1.5%, and containing Mn:0.1~0.8%, Zr:0.04~0.20%, Cr:0.04~
0.20%, Sc:0.02~0.1% one or more of be used as transition elements, surplus by Al and inevitably it is miscellaneous
Texture at.In addition, the % of the content of each element indicates the meaning of entirely quality %.
Illustrate below each element in above-mentioned 6000 line aluminium alloy containing range and meaning or allowance.
Mg:0.3~1.5%
Mg facilitates solution strengthening together with Si, and in the artificial aging processing of coating baking processing etc., is formed with
Help intensity raising precipitation, play age hardening capability, be for obtaining the structural elements as automobile etc. needed for
The necessary element of the yield strength wanted.
When Mg content is lower than 0.3%, intensity is insufficient.On the other hand, if Mg content is higher than 1.5%, shear band when cold rolling
It is easy to form, the reason of becoming crackle when rolling.Therefore, Mg content is 0.3% or more, preferably 0.4% or more, and
1.5% hereinafter, preferably 1.2% range below.
Si:0.3~1.5%
Si facilitates solution strengthening and in the artificial aging processing of coating baking processing etc., is formed with together with Mg
Help intensity raising precipitation, play age hardening capability, be for obtaining the structural elements as automobile etc. needed for
The necessary element for the intensity (yield strength) wanted.
When Si content is lower than 0.3%, intensity is insufficient.On the other hand, if Si content is higher than 1.5%, coarse change is formed
Object is closed, ductility is deteriorated.Therefore, Si content is 0.3% or more, preferably 0.7% or more, and 1.5% hereinafter, preferably
1.4% range below.
Mn、Zr、Cr、Sc
The transition elements of Mn, Zr, Cr, Sc are the main members for constituting transition elements system dispersed granules specified in the present invention
Element.It forms transition elements system dispersed granules in the stage and final plate of ingot bar, and crystal grain is made to miniaturize and propose intensity
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 is improved, with the structure after forming
The raising of artificial age-hardening's ability (BH) of component combines, and significantly improves the intensity after BH.
If the content of Mn, Zr, Cr, Sc are very few, the number density of the dispersed granules is reduced, when plate is shaped to structural elements
Processing hardening and artificial age-hardening's ability (BH) reduce, the increase of yield strength resulting from reduces, described
Synergy becomes smaller, and treated that intensity can not increase to level required by structural elements for artificial aging.
On the other hand, if Mn, Zr, Cr, Sc content are excessive, coarse compound easy to form easily becomes destruction
Starting point makes ductility and strength deterioration instead.
Therefore, containing Mn:0.1~0.8%, Zr:0.04~0.20%, Cr:0.04~0.20%, Sc:0.02~0.1%
One or more of.
Other elements
In addition, in the present invention, in order to enable aluminum alloy to plate high intensity, (but can also be free of containing Cu:0.5% or less
0%), one or more of Ag:0.01~0.2%, Sn:0.001~0.1%.
Subsidiary one mentions, because these elements have the effect of 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, have in the opposite crystal grain of compound for promoting area board group Zhi GP etc.
The effect of precipitation.Sn has the effect that, captures atom vacancy, thus inhibits the diffusion of Mg and Si at room temperature, inhibits room temperature
Under intensity increase (room-temperature aging), in artificial aging processing, discharge the vacancy of capture, promote the diffusion of Mg and Si, improve
BH.
But if the respective content of these elements is excessive, coarse compound etc. is formed, the manufacture of plate is difficult, intensity
It is reduced with bendability, in addition, corrosion resistance also reduces.If especially Cu content is excessive, bendability is significantly reduced.
Therefore, contain these elements sometimes, be each upper limit value content below.
Impurity
Other Fe, V, Ti, B, Zn etc., be easy it is 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 be allowed to for the specification of JIS etc. it is permitted
Content.For example, being preferably 0.5% or less about Fe.
(tissue)
After becoming the chemical component composition that above 6000 are alloy, in the present invention, it is specified that this 6000 is that aluminium closes
The tissue of golden plate.That is, so that the average crystal grain diameter of the plate thickness central part of the plate it is tiny it is (small) premised on, make described fine
Transition elements system dispersed granules real mass exists, and provides its average equivalent circular diameter and average number density together.
These organization prescribeds are formed and manufacturing condition with not changing existing aluminium alloy substantially, 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:
Keep the average crystal grain diameter of plate thickness central part tiny (small), becoming makes the fine transition elements system disperse grain
The effect of son is able to the precondition played.That is, the grain structure of plate thickness central part, is average crystal grain diameter at 100 μm or less
Fine grain structure when, the effect of the fine transition elements system dispersed granules starts to play.The crystalline substance of plate thickness central part
Grain tissue, when being higher than 100 μm of coarse 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 guarantee fine transition elements system dispersed granules
The precondition that effect plays.
Described crystal grain diameter in the present invention is the longitudinal section (plate cut off along rolling direction in the rolling direction of plate
Section) in, the crystal grain diameter of the rolling direction of plate thickness central part.The measurement of the average crystal grain diameter is to pass through rolling direction
Line-intercept method evaluated.That is, being by extracting the longitudinal section from the plate quenched through T4 being configured to before structural elements
Plate thickness central part sample, to sample surface carry out mechanical lapping after, tetrafluoro boric acid: in water=5:400 solution, with voltage
30V, 20~30 DEG C of solution temperature, the progress electrolytic etching of 60~90 seconds time.Then, by using 50 times of light of polarizing film
Microscope is learned, for the arbitrary measurement position of plate thickness central part due in view of the deviation of the material of plate, passes through 10 visuals field
The visual observation of (every 5,1 visual field, every 500 μm of 1 wire length) carries out.
Transition elements system dispersed granules:
Using above average crystal grain diameter as premise, the tissue of the plate thickness central part as plate, with 50,000 times of multiplying power
TEM-EDX measurement, range that the average equivalent circular diameters of transition elements system dispersed granules are in 50~300nm, also, equivalent
Circular diameter is 5/μm in the average number density of the transition elements system dispersed granules of the range of 20~400nm3More than.
In the tissue of 6000 line aluminium alloy plates before artificial aging processing, make the average equivalent of transition elements system dispersed granules
Circular diameter is the range of 50~300nm, also, has the fine transition elements of the equivalent circle diameter of the range of 20~400nm
It is that dispersed granules exist as much as possible, and 5/μm of density that average out3(exist more) when above, is then mentioned 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 being equivalent at the heat of baking painting treatment
Recovery when reason inhibits, and the transition elements system dispersed granules of the size and number density are especially helpful.Moreover, such micro-
Thin transition elements system dispersed granules, the effect for also having the formability that former material plate will not be hindered to be configured to structural elements excellent in this way
Fruit.
The transition elements system dispersed granules with average equivalent circular diameter, or the equivalent circle diameter with the range
Transition elements system dispersed granules, heating when not only being handled via artificial aging make yield strength (intensity) improve, but also
Processing hardening when shaping from the former material plate of its leading portion to automotive structural members improves.The fine transition elements as a result,
It is dispersed granules, the raising of processing hardening when being shaped by former material plate to automotive structural members, and the automobile knot after forming
The synergy of the raising of artificial age-hardening's ability of structure component, and significantly improve BH.
Otherwise the average equivalent circular diameter of either transition elements system dispersed granules is as low as lower than 50nm, in addition, coarsening
And it is higher than 300nm, the synergy that the intensity after the BH improves all can not play or become smaller.
In addition, the fine transition elements system dispersed granules of the equivalent circle diameter of the range with 20~400nm are averaged
Number density is lower than 5/μm3When, the number of the fine transition elements system dispersed granules is very few, and the synergy can not be sent out
It waves.In the present invention, no matter large or small (equivalent circle diameter), not providing can be by the TEM-EDX of 50,000 times of multiplying power measurement
The average number density of transition elements system dispersed granules.
In addition, if there is the fine mistake of the equivalent circle diameter of the range of the 20~400nm from the boundary of manufacture
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 transition elements system dispersed granules fine in this way tails off, and reason is the transition member constituted
Cellulose content is insufficient.But in addition to this, though constitute transition elements content content it is appropriate, due to plate preparation method the problem of,
Also the transition elements system dispersed granules for having generation cannot be grown, and equivalent circle diameter is too small (meticulous) without 20nm, or vice versa
Excessively coarsening and a possibility that be higher than 400nm etc..
The measurement of transition elements system dispersed granules:
The fine transition elements system of the equivalent circle diameter of the range with 20~400nm specified in the present invention is more
Shot average number density (it is a/μm3), by the EDX that possesses for identifying (identification) dispersed granules, (energy dispersion type X is penetrated
Line optical spectroscopy) function 50,000 times of multiplying power TEM (transmission electron microscope: FE-TEM) measurement.
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 material), processing hardening also becomes problem, thus for for being shaped by bending machining etc. plus
Work is the aluminium alloy plate before used structural elements.
Specific measurement method is to extract the sample of plate thickness central part from the T4 material before the forming, TEM is being made
After film sample, by the macrograph of the TEM shooting plate thickness central part 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) it can identify can measure with equivalent circle diameter for (identification)
The equivalent circle diameter 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 equivalent circle diameter enclosed average number density (it is a/μm3)。
Here, in the measurement of the average equivalent circular diameter and average number density, for being mentioned from arbitrary plate thickness central part
10 samples taken carry out, and are equalized, and the transition elements system of the equivalent circle diameter as the range with 20~400nm is more
Shot average number density (it is a/μm3)。
Described transition elements system dispersed granules, are the visuals field for the plate thickness central part by tem observation in the present invention, are used
X-ray spectrometry device (EDX) is analyzed, and identifies the transition containing one or more of Mn, Cr, Zr, Sc accordingly
First prime system dispersed granules (precipitate) identify other precipitates (dispersed granules) without these transition elements.Carry out this knowledge
When other, the amount containing one or more of Mn, Cr, Zr, Sc, as long as the amount that can be detected by the EDX is (micro-
Amount), if from the precipitate in the visual field, by the EDX be capable of detecting when one of Mn, Cr, Zr, Sc or
It is two or more, it is all transition elements system dispersed granules described in the present invention no matter then its amount.
Here, so-called equivalent circle diameter, is exactly using the EDX, identifying (can identify), it is containing Mn, Cr, Zr, Sc
One or more of transition elements system dispersed granules, image procossing is carried out to this dispersed granules, calculates TEM view
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
Diameter) (circle equivalent diameter).
(manufacturing method)
Then, it is illustrated below for the manufacturing method of aluminium alloy plate of the present invention.Aluminium alloy plate of the present invention, manufacturing process
It itself is that conventional method or well known method homogenize after casting above-mentioned 6000 is tied to form the aluminium alloy ingot bar being grouped as
Heat treatment, and implement hot rolling, cold rolling and become defined plate thickness, then implement solutionizing quenching treatment etc. modifier treatment and make
It makes.
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 preferred manufacturing condition.
(fusing, casting cooling speed)
Firstly, adjusting fusing to the melting Al in above-mentioned 6000 set member compositing range in fusing, casting process
Alloy is suitable for that the common melting and casting method of continuously casting rolling, semi-continuous casting method (DC casting) etc. is selected to be cast
It makes.
(homogenize heat treatment)
Secondly, before hot rolling, implementing the heat treatment that homogenizes for the aluminium alloy ingot bar cast.This homogenizes
It is heat-treated (homogeneous heat treatment), in addition to general object, i.e. tissue homogenizes and (eliminates the segregation in the crystal grain in ingot bar tissue)
In addition, it is important that miniaturize transition elements system dispersed granules to nanoscale and in other words exactly avoid its coarsening.
Therefore, equal heat condition can be a homogeneous heat treatment, be also possible to secondary soaking or two sections of soaking, but its heating,
Cooling procedure needs to control.
So-called secondary soaking is exactly 200 DEG C of temperature below being first cooled to including room temperature after first time soaking
Degree, then reheated, it maintains after a certain period of time, to start hot rolling with this temperature.In contrast, so-called two sections of soaking, be exactly
Although being cooled down after first time soaking, be not cooled to 200 DEG C hereinafter, but higher temperature stop it is cooling after, 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 segment hankered, be 500 DEG C with
The temperature range of fusing point is gone up and be lower than, in order to inhibit the coarsening of transition elements system dispersed granules, is controlled in defined ruler
It is suitable for selecting from 1 minute or more and in the range of 1 hour retention time below under very little and number density.
Heating rate when the first segment soaking of the first time or two sections of soaking of this soaking or secondary soaking is 100
DEG C/instant heating of hr or more, it is precipitated to make transition elements system dispersed granules nanoscale as fine to described as possible, preferably
Accelerate heating rate.It is lower than 100 DEG C/hr if heating rate is slow, transition elements system dispersed granules coarsening, having cannot to the greatest extent can
Can the nanoscale and a possibility that be precipitated.
On the other hand, the cooling velocity after the first time soaking of secondary soaking, it is cold after the first segment soaking of two sections of soaking
But speed is 40 DEG C/hr hereinafter, preferably 30 DEG C/hr outside furnace hereinafter, it is preferred that do not let cool, but lets cool in furnace, and normal
Rule method is on the contrary, keep cooling velocity as small as possible (slow).
The precipitation and growth for the transition elements system dispersed granules for promoting the nanoscale in cooling fine as a result, will
It is controlled in defined size and number density.
In addition, primary in thermal process, cooling velocity after a homogeneous heat treatment is it is also preferred that as small as possible (slow)
40 DEG C/the hr or less.
Second or the equal heat condition of second segment, preferably more than hot rolling start temperature and 500 DEG C of temperature ranges below,
The range of 30 minutes or more retention times selects, and reheats first time soaking, ingot bar after cooling, is cooled to hot rolling and starts temperature
Degree, or it is again heated to hot rolling start temperature, it is kept in this neighborhood.Alternatively, it is also possible to which the ingot bar after first segment soaking is cooled to
Hot rolling start temperature is kept in this neighborhood.This second or second segment soaking temperature, than for the first time or first segment soaking temperature
It is low.In addition, to the time of hot rolling start temperature after control soaking, can also obtain same effect in primary heat condition.
In addition, about the cooling velocity for the second time or after the heating of the soaking temperature of second segment, soaking, because described
First time or the equal thermal process of first segment in form the transition elements system dispersed granules of desired morphology, so if it is meet with
The scope of the lower hot-rolled condition, then do not need that heating rate and cooling velocity is especially made to be in identical condition and range.
(hot rolling)
Homogenize heat treatment ingot bar hot rolling, according to the plate thickness of rolling, by the roughing operation of ingot bar (slab)
It is constituted with finish to gauge process.It is suitable for the milling train using reversible or tandem etc. in this roughing operation and finish to gauge process.
The start temperature of hot roughing as hot rolling start temperature, it is primary in thermal process preferably 350 DEG C or more and
Solidus temperature is hereinafter, be preferably 350 DEG C or more and 400 DEG C or less in secondary equal thermal process.The start temperature of hot roughing is low
When 350 DEG C, any its hot rolling of thermal process material is difficult, otherwise be higher than 400 DEG C, in secondary equal thermal process material, and transition
First coarse precipitation of prime system dispersed granules, cannot nanoscale as fine to described as possible and height a possibility that be precipitated.In addition, about one
Secondary equal thermal process material makes soaking time after the progress of defined time range, carries out hot rolling immediately, so as to inhibit transition first
The coarsening of prime system dispersed granules carries out hot rolling in the state of maintaining the transition elements system dispersed granules of desired form.
After such hot roughing, preferably carry out terminating temperature in the hot finish to gauge of 300~350 DEG C of range.The hot finish to gauge
End temperature it is too low and when being lower than 300 DEG C, rolling loads are high, and productivity reduces.On the other hand, in order not to a large amount of residual process
It organizes and becomes recrystallized structure, when improving the end temperature of hot finish to gauge thus, if its temperature is higher than 350 DEG C, transition elements
A possibility that being the coarse precipitation of dispersed granules, nanoscale as fine to described as possible cannot be allowed to and be precipitated height.
(annealing of hot rolled plate)
The hot rolled plate does not need to anneal (black annealing) before cold rolling, but can be implemented yet.
(cold rolling)
In cold rolling, above-mentioned hot rolled plate is rolled, is fabricated to the cold-reduced sheet (also including coiled material) of desired final plate thickness.But
It is, in order to miniaturize crystal grain more, it is desirable to cold rolling rate is 30% or more, in addition for purpose same as 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, the quenching treatment of room temperature is next proceeded to.At this solutionizing quenching
Reason, can be used common continuous heat-treatment lines.But the sufficient solid solution capacity of each element of Mg, Si etc. in order to obtain, preferably
After carrying out solutionizing processing under 550 DEG C or more and melting temperature temperature below, make to the average cooling rate 20 of room temperature
DEG C/sec or more.At a temperature of lower than 550 DEG C, solutionizing handle previous existence at the compound of Mg-Si system etc. be dissolved again not
Sufficiently, being dissolved Mg amount and solid solution Si amount reduces.
In addition, mainly generating the precipitate of Mg-Si system in cooling when average cooling rate is lower than 20 DEG C/sec, it is dissolved Mg
A possibility that amount and solid solution Si amount reduce, cannot ensure the solid solution capacity of Si and Mg is still high.In order to ensure the cooling velocity, quenching
Selection uses the air-cooled of fan etc., the water cooling means and condition of spraying, spray, impregnating etc. respectively for processing.
(Pre-aging treatment: reheating processing)
Be quenched after such solutionizing processing and after being cooled to room temperature, preferably to cold rolling within 1 hour
Plate carries out Pre-aging treatment (reheating processing).To room temperature quenching treatment after, if starting to Pre-aging treatment, (heating is opened
Begin) room temperature i time it is too long, then due to room-temperature aging, cause the Mg-Si cluster of rich Si to generate, it is difficult to make Mg's and Si
Good Mg-Si cluster is balanced to increase.Therefore, the shorter the room temperature i time the better, solutionizing and quenching treatment and reheat
Processing, can also be carried out continuously, the time of lower limit does not set especially almost without the time difference.
The Pre-aging treatment preferably makes retention time 5 hours or more at 60~120 DEG C and 40 hours or less and carries out
It keeps.The good Mg-Si cluster of balance of Mg and Si can be formed as a result,.
If pre-age temperature is lower than 10 hours lower than 60 DEG C or retention time, the case where with no Pre-aging treatment
Equally, it is difficult to inhibit the Mg-Si cluster of richness Si, it is difficult to which the Mg-Si cluster for making the Mg and Si keep balance increases, and baking applies
Yield strength after dress is easy to be lower.
On the other hand, preageing condition is higher than 120 DEG C, or more than 40 hours, the production quantity that core is precipitated was excessive, toasts coating
Intensity when preceding bending machining becomes excessively high, and bendability is easy deterioration.
Hereinafter, enumerating embodiment further illustrates the present invention, the present invention is not limited certainly by following embodiments, can
The range of aftermentioned objective can also suitably be changed implementation before meeting, these are all contained in technical scope of the invention
It is interior.
Embodiment
As the embodiment of the present invention, changes composition and manufacturing condition, manufacture the fine transition of the nanoscale respectively
The average number density of the first prime system dispersed granules 6000 line aluminium alloy plates different with average crystal grain diameter.Then, it measures, evaluate plate
BH (coating baking hardening) after manufacture.It is as the result is shown in table 1,2,3.
The specific manufacturing method respectively, for 6000 line aluminium alloy plates of composition shown in table 1, such as 2,3 institute of table
Show, the manufacturing condition of equal heat condition and hot roughing start temperature etc. is made to carry out various changes.
Here, the numerical value of each element is what blank was shown in the expression of the content of each element in table 1, its content is indicated
(0%) below detectable limit.
The specific manufacturing condition of aluminium alloy plate is as follows.For the aluminium alloy ingot bar respectively formed shown in table 1, commonly through
DC casting melting.Next, for ingot bar, after each example carries out homogeneous heat treatment with each different condition shown in table 2,3,
Start hot roughing with each different temperatures shown in table 2,3.
Then, each example is common, terminate temperature in the hot finish to gauge of 300~350 DEG C of range, all becomes thickness
The hot rolled plate of 4.0mm.For hot rolled plate, each example without the intermediate annealing of black annealing and cold rolling pass on the way after hot rolling, and
Carry out the cold rolling of working modulus 50%, the cold-reduced sheet as thickness 2.0mm.
Again for each cold-reduced sheet, with each example condition all the same, modifier treatment (T4) is carried out with Equipment for Heating Processing.It is specific next
It says, with progress solutionizing processing in 550 DEG C × 30 minutes, at this moment, until the average heating rate of 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
Later, the condition kept for 8 hours with 100 DEG C immediately carries out Pre-aging treatment, slow cooling (letting cool) after Pre-aging treatment.
To cut on each final product plate after being placed at room temperature for 2 weeks for test plate (panel) (blank) after these modifier treatment, according to
The measurement method measures the average equivalent circular diameter (nm) of each transition elements system dispersed granules for test plate (panel), and have 20~
The transition elements system dispersed granules of the equivalent circle diameter of the range of 400nm average number density (it is a/μm3), average crystal grain diameter
The tissue of (μm) etc..
In addition, measuring, evaluating each BH for test plate (panel).These are as the result is shown in table 2,3.
(BH)
By tension test, acquire respectively it is described respectively for 0.2% yield strength of test plate (panel) (As yield strength: T4 material=at
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 is the stretching for simulating bending machining to the forming 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 strength is sequentially shown, 0.2% yield strength after 2% stretching
Incrementss, 0.2% yield strength after the BH.
In the tension test, from described respectively on test plate (panel), extract respectively JIS Z 2201 No. 5 test films (25mm ×
50mmGL × plate thickness), tension test is carried out at room temperature.Make the draw direction of test film at this moment side parallel with rolling direction
To.In addition, tensile speed 5mm/ points, being carried out under certain speed until test film is broken with gauge length 50mm.Mechanical characteristic
The N number of measurement is 5, respectively with mean value calculation.
If table 1,2 is respectively shown in, each example 1~13 is in ingredient compositing range of the invention, and in preferred item
The manufacture of part range.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, equivalent circle diameter be 20~400nm range transition elements system dispersed granules average number density,
Average crystal grain diameter).
Its result is it is found that these each examples, even if as shown in table 2,0.2% surrender after BH is strong after room-temperature aging
Degree is also high, for high intensity.That is, described 2% stretch after the incrementss of 0.2% yield strength be up to 33MPa or more, former material plate to
Processing hardening when automotive structural members shape improves.
And it is found that is mentioned by with the yield strength (intensity) when the processing of the artificial aging of the automotive structural members after forming
High synergy, BH improve significantly to 262MPa or more.
In contrast, the comparative example 14~21 of table 3, uses alloy example 1,4 identical with the example of 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. is detached from preferred condition.
Its soaking temperature of comparative example 14 is too low and is lower than 500 DEG C.
Heating rate when 15,18,21 its soaking of comparative example is excessively slow and is lower 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 equal thermal process, but hot roughing start temperature it is excessively high and more than 400 DEG C.
Comparative example 17,20 is secondary equal thermal process, but the start temperature of hot roughing is too low and be lower than 350 DEG C.
Therefore, these comparative examples, equivalent circle diameter are the flat of the transition elements system dispersed granules of the range of 20~400nm
Equal number density, average crystal grain diameter, are detached from tissue given to this invention.
As a result, 0.2% yield strength compared with the example formed as same alloy, after 2% stretching
Even if incrementss it is high, also down to 30MPa or so, the synergy improved with yield strength when BH cannot be played, 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 is manufactured in preferred condition and range, the composition of alloy of table 1 is used to distinguish
It is detached from the alloy number 9~14 of the scope of the invention.
Comparative example 22,23 is that the content of Mn, Zr, Cr, Sc of the alloy number 9,10 of table 1 are very few.
Comparative example 24 is the alloy number 11 of table 1, and the content of Mg is very few.
Comparative example 25 is the alloy number 12 of table 1, and the content of Mg is excessive.
Comparative example 26 is the alloy number 13 of table 1, and the content of Si is very few.
Comparative example 27 is the alloy number 14 of table 1, and the content of Si is excessive.
Therefore, these comparative examples are as shown in table 3, transition elements system disperse of the equivalent circle diameter in the range of 20~400nm
Average number density, average crystal grain diameter of particle etc. are detached from from tissue given to this invention.
Even if as a result, described 2% stretch after 0.2% yield strength incrementss it is high, also down to 30MPa or so,
The synergy improved with yield strength when BH cannot play, also poor to 244MPa even if the BH after room-temperature aging is high
Left and right.
Therefore, for high intensity, also there is whole as a result, it was confirmed that even if after room-temperature aging by above embodiment
Meet the necessity of composition and tissue given to this invention.
[table 1]
In detail and the present invention is illustrated referring 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 based on Japanese patent application (patent application 2015-108596) filed on May 28th, 2015, in
Hold reference herein to be incorporated into.
Industrial availability
In accordance with the invention it is possible to provide 6000 line aluminium alloy plates of high intensity.As a result, other than panel material,
6000 line aluminium alloy plates can also as vehicle frame, beam column etc. skeleton material or, bumper bar armature, door anti-collision joist etc. reinforcement
The automotive structural members of material etc. and expand its application.
Claims (2)
1. a kind of high-strength aluminium alloy plate, which is characterized in that be following Al-Mg-Si-type aluminum alloy plate, in terms of quality %
Contain Mg:0.3~1.5%, Si:0.3~1.5% respectively, and contain Mn:0.1~0.8%, Zr:0.04~0.20%, Cr:
0.04~0.20%, Sc:0.02~0.1% one or more of be used as transition elements, surplus is by that Al and can not keep away
The impurity exempted from is constituted,
The tissue of plate thickness central part as the plate, average crystal grain diameter is at 100 μm hereinafter, and with 50,000 times of multiplying power
The average equivalent circular diameter of dispersed granules that TEM-EDX is measured, containing the transition elements is the range of 50~300nm,
Also, equivalent circle diameter is 5/μm in the average number density of the transition elements system dispersed granules of the range of 20~400nm3With
On.
2. high-strength aluminium alloy plate according to claim 1, wherein the aluminium alloy plate also contain Cu:0.5% or less but
Without one or more of 0%, Ag:0.01~0.2%, Sn:0.001~0.1%.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2015-108596 | 2015-05-28 | ||
| JP2015108596A JP6810508B2 (en) | 2015-05-28 | 2015-05-28 | High-strength aluminum alloy plate |
| PCT/JP2016/065682 WO2016190409A1 (en) | 2015-05-28 | 2016-05-27 | High-strength aluminum alloy plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN107532247A CN107532247A (en) | 2018-01-02 |
| CN107532247B true 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) |
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| 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 |
| CA3064022C (en) * | 2017-05-26 | 2023-06-27 | Novelis Inc. | 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 |
| 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 |
| 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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| 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 |
| JP2009173973A (en) * | 2008-01-22 | 2009-08-06 | Kobe Steel Ltd | Aluminum alloy sheet having excellent ridging mark property upon forming |
| WO2014126073A1 (en) * | 2013-02-13 | 2014-08-21 | 株式会社神戸製鋼所 | Aluminum alloy sheet with excellent baking paint hardenability |
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| US6231809B1 (en) * | 1998-02-20 | 2001-05-15 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Al-Mg-Si aluminum alloy sheet for forming having good surface properties with controlled texture |
| EP1788103B1 (en) * | 1998-09-10 | 2014-12-31 | Kabushiki Kaisha Kobe Seiko Sho | Al-Mg-Si based alloy sheet |
| JP3802695B2 (en) * | 1998-11-12 | 2006-07-26 | 株式会社神戸製鋼所 | Aluminum alloy plate with excellent press formability and hemmability |
| JP4499369B2 (en) * | 2003-03-27 | 2010-07-07 | 株式会社神戸製鋼所 | Al-Mg-Si-based alloy plate with excellent surface properties with reduced generation of ridging marks |
| KR101103135B1 (en) * | 2005-05-25 | 2012-01-04 | 니폰게이긴조쿠가부시키가이샤 | Aluminum alloy sheet and method for manufacturing the same |
| US8932728B2 (en) * | 2012-03-15 | 2015-01-13 | Kobe Steel, Ltd. | Aluminum-alloy clad sheet |
| WO2014155818A1 (en) * | 2013-03-29 | 2014-10-02 | 古河電気工業株式会社 | Aluminum alloy conductor, aluminum alloy twisted wire, coated electric wire, wire harness, and production method for aluminum alloy conductor |
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2015
- 2015-05-28 JP JP2015108596A patent/JP6810508B2/en active Active
-
2016
- 2016-05-27 US US15/573,887 patent/US20180363113A1/en not_active Abandoned
- 2016-05-27 CN CN201680024760.3A patent/CN107532247B/en not_active Expired - Fee Related
- 2016-05-27 WO PCT/JP2016/065682 patent/WO2016190409A1/en active Application Filing
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| JP2009173973A (en) * | 2008-01-22 | 2009-08-06 | Kobe Steel Ltd | Aluminum alloy sheet having excellent ridging mark property upon forming |
| WO2014126073A1 (en) * | 2013-02-13 | 2014-08-21 | 株式会社神戸製鋼所 | Aluminum alloy sheet with excellent baking paint hardenability |
| CN104981555A (en) * | 2013-02-13 | 2015-10-14 | 株式会社神户制钢所 | Aluminum alloy sheet with excellent baking paint hardenability |
Also Published As
| Publication number | Publication date |
|---|---|
| US20180363113A1 (en) | 2018-12-20 |
| JP6810508B2 (en) | 2021-01-06 |
| CN107532247A (en) | 2018-01-02 |
| JP2016222959A (en) | 2016-12-28 |
| WO2016190409A1 (en) | 2016-12-01 |
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