CN106661680B - Aluminium alloy plate - Google Patents
Aluminium alloy plate Download PDFInfo
- Publication number
- CN106661680B CN106661680B CN201580043382.9A CN201580043382A CN106661680B CN 106661680 B CN106661680 B CN 106661680B CN 201580043382 A CN201580043382 A CN 201580043382A CN 106661680 B CN106661680 B CN 106661680B
- Authority
- CN
- China
- Prior art keywords
- mentioned
- compounds
- aluminium alloy
- plate
- temperature
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—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
-
- 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
-
- 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
-
- 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
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Shaping Metal By Deep-Drawing, Or The Like (AREA)
- Body Structure For Vehicles (AREA)
- Laminated Bodies (AREA)
- Metal Rolling (AREA)
- Continuous Casting (AREA)
Abstract
The present invention relates to a kind of aluminium alloy plates, which is characterized in that it is to include Mg respectively in terms of quality %：0.3~1.0%, Si：0.5~1.5%, Sn：0.005~0.2%, Fe：0.02~1.0% and Mn：0.02~0.6%, and the Al-Mg-Si-type aluminum alloy plate that surplus is made of Al and inevitable impurity, wherein, tissue as above-mentioned aluminium alloy plate, it is measured using 500 times of SEM, in the compound identified using X-ray spectrum device, the content containing Mn and Fe, Sn is that the average number density of the Sn compounds for the range that more than 1.0 mass % and equivalent circle diameter is 0.3~20 μm is 500~3000/mm2Range, and the length at the interface of above-mentioned Sn compounds and aluminium base by the value obtained by the measure area of the overall circumference of above-mentioned Sn compounds divided by above-mentioned SEM come in terms of 3~20/mm of average out to range.The aluminium alloy plate of the present invention disposes the requirement of formability, BH after the room-temperature aging as automobile outer panels, and filiform corrosion resistance is also excellent.
Description
Technical field
The present invention relates to a kind of Al-Mg-Si-type aluminum alloy plate more particularly to formability, BH and excellent corrosion resistances
Aluminium alloy plate.Described aluminium alloy plate is the milled sheets such as hot rolled plate and cold-reduced sheet in the present invention, refers to implementing solid solution
Aluminium alloy plate after processing and quenching treatment etc. are quenched and before baking application cure process is carried out.In addition, following
Aluminium is also referred to as Al in record.
Background technology
In recent years, it is contemplated that the light-weighted social desirability of the vehicles such as earth environment etc., automobile is higher and higher.In order to cope with
This requirement, large-scale body panel (outer panels, inner panel) as car panel, particularly hood, car door, roof etc.
Material, instead of the steel material of steel plate etc., application hardenability is excellent and the application of the aluminium alloy material of more light weight for formability and baking
Increasing.
In the large car dignity panel structure of the automobile, have studied in hood, mud guard, car door, roof, luggage case
The 6000 line aluminium alloy plate of AA or even JIS of Al-Mg-Si systems is also used as thin-walled and height in the outer panels (outside plate) of lid etc.
Strength aluminum alloy sheets.
It is well known that above-mentioned automobile outer panels are stamping by progress compound to the 6000 line aluminium alloy plates for being used as former material
In expansion forming when, the forming such as bending forming make.For example, in the outer panels of the large size such as hood and car door,
By the stamping of expansion etc., the formed products shape as outer panels is formed, then, passes through the flat volume of the outer panels peripheral portion
Crimping (hemming) processing on side etc., carries out the engagement with inner panel, and as panel structure.
6000 line aluminium alloy has the advantages that have excellent BH (baking hardenability), and on the other hand, have
Room-temperature aging is kept using solution hardening treated room temperature and age-hardening occurs, increases intensity, thus there are opposites
The subject that the formability of plate reduces.And then it can also generate problems with：In the case where such room-temperature aging is big, BH is reduced,
Using heating of the coating baking processing of the panel after forming when the artificial aging (hardening) compared with low temperature is handled, yield strength is still
It can not be increased to as the required intensity of panel.
It proposes largely, as one of them, to be included in 6000 line aluminium alloy plates to its metallurgical countermeasure all the time
In actively add Sn realize room-temperature aging inhibition and BH raising method.For example, it proposes in patent document 1 logical
It crosses and adds appropriate Sn and implement preliminary aging after solution treatment and have both room-temperature aging inhibition and the method for BH.Separately
Outside, following methods are proposed in patent document 2：Sn is added in 6000 line aluminium alloy plates and improves the Cu of formability, so as to carry
High formability, baking coating, corrosion resistance.
Existing technical literature
Patent document
Patent document 1：Japanese Unexamined Patent Publication 09-249950 bulletins
Patent document 2：Japanese Unexamined Patent Publication 10-226894 bulletins
Invention content
The subject that the invention solves
With regard to these it is previous be actively added to the 6000 line aluminium alloy plates of Sn for, the original of the outer panels as automobile
Material, in the compound good formability having both after prolonged room-temperature aging and high BH and excellent filiform corrosion resistance
Etc. there is still room for improvement in many characteristics.
For example, the raising of filiform corrosion resistance is necessary (for the external panel used) for automobile outer panels.Vapour
Vehicle outer panels reuse after being although coated, but are exposed and corrode ring in seawater, brine of the running environment as automobile etc.
In border (corrosive environment under film).Accordingly, there exist problems with：Aluminium alloy plate surface under film generates and grows to be claimed
Make the Filamentous rust of the precipitate, field trash of filiform corrosion as starting point, cause reduction and the bad order of the intensity of component.Cause
This, in order to which the Al-Mg-Si-type aluminum alloy plate for being added to Sn is used in automobile outer panels, it is necessary to have excellent resistance to filiforms
It is tarnish resistance.
In the past, it is also proposed that the composition of the various base material sides for improving filiform corrosion resistance, tissue in 6000 line aluminium alloy plates
Deng improving environment.But metallurgical behavior when being added to Sn has difference with the situation for not adding Sn, not really
Whether the improving environment of fixed above-mentioned previous base material side is also effective in the case where adding Sn on earth.Therefore, in order to make actively to add
The filiform corrosion resistance of the 6000 line aluminium alloy plates of Sn has been added to be improved together with other above-mentioned characteristics such as formability, BH, has been needed
Seek the improvement alternative individually to the 6000 line aluminium alloy plates for adding Sn.
In addition, in above-mentioned formability, there is also required by the 6000 line aluminium alloy plate of former material of the outer panels to automobile
The increasingly harsh tendency of subject.The outer panels of automobile need directly to embody strainless beautiful curved surface composition and designed spy
Sign.This is the problem as caused by outer panels unique design, in outer panel mounting knob seat, lamp holder, license (car plate) seat etc.
The recess portion (expanding section, embossed portion) of utensil or component or partly the setting prescribed depth as describing wheel arch.
To such recess portion together with around the recess shapes continuous curved surface carry out it is stamping in the case of, shaping
Property 6000 line aluminium alloy plates poorer than steel plate in easy generate face strain, it is difficult to realize above-mentioned strainless beautiful curved surface form and
Feature.Therefore, in 6000 line aluminium alloy plates, in the generation to the face must be inhibited to strain during the formings of automobile outer panels.This
The problem of the problem of kind of face strain is not only above-mentioned recess portion (expanding section) but also be the saddle of door outer panel, front
The disappearance portion of feature outside the longitudinal wall part of mud plate, the wind corner of rear mudguard, luggage-boot lid or hood, rear mud guarding sheet-pile
The common subject of car panel as the parts such as installation base portion have the recess portion (expanding section) that can generate face strain.
For such subject, in order to inhibit the generation of above-mentioned face strain, it is expected to reduce when being stamped into shape (after fabrication
For room-temperature aging) 0.2% yield strength of 6000 line aluminium alloy plates.But surrender when if so reducing stamping is strong
Degree is then difficult to obtain the high-yield strength after baking application cure process (baking hardening) instead.
The present invention is to solve such subject and the invention completed, and its purpose is to provide dispose as outside automobile
The requirement of formability, BH after the above-mentioned room-temperature aging of plate and 6000 systems containing Sn for also improving filiform corrosion resistance
Aluminium alloy plate.
Means for solving the problems
In order to reach the purpose, being intended to of aluminium alloy plate of the invention provides a kind of aluminium alloy plate, is with matter
It measures % meters and includes Mg respectively：0.3~1.0%, Si：0.5~1.5%, Sn：0.005~0.2%, Fe：0.02~1.0% and Mn：
0.02~0.6% and the Al-Mg-Si-type aluminum alloy plate that is made of Al and inevitable impurity of surplus, it is closed as above-mentioned aluminium
The tissue of golden plate is measured using 500 times of SEM, in the compound identified using X-ray spectrum device, containing Mn and
The content of Fe, Sn are the average number density of the Sn compounds for the range that more than 1.0 mass % and equivalent circle diameter is 0.3~20 μm
For 500~3000/mm2Range, and the length at the interface of above-mentioned Sn compounds and aluminium base is with above-mentioned Sn compounds
Value obtained by the measure area of overall circumference divided by above-mentioned SEM counts the range of 3~20/mm of average out to.
Invention effect
In the tissue of 6000 line aluminium alloy plates, Sn has the work that atomic vacancy (capturing, trap) is captured in room temperature state
With.Using the effect of the Sn, inhibiting the diffusion in Mg, Si of room temperature, inhibit room-temperature aging (hardening), inhibition strength increases,
The effect for improving the press formabilities such as crimping processability, deep-draw processing, expansion processing is also brought when plate is configured to panel.The opposing party
Face is handled in the coating baking of panel when artificial agings are handled, and Sn also has the following effects that：Since captured sky can be discharged
Cave, therefore promote the diffusion of Mg or Si instead, BH can be improved.
But according to the opinion of the inventors of the present invention, the capture of the atomic vacancy of these Sn, releasing effect are initially by making Sn
It is solid-solution in base material and plays.However, the solid solution capacities of Sn in the substrate are few (low), using the manufacturing method of common plate, i.e.,
Make to inhibit the additive amount of Sn in theoretical solid solution capacity hereinafter, it is not also dissolved and crystallization or analysis in the form of compound largely
Go out.Although do not have in this way with the improvement effect of compound form crystallization or the Sn of precipitation with aftermentioned filiform corrosion resistance
There are capture, the releasing effect of atomic vacancy.
Therefore, in the present invention, the manufacturing method of plate is also after check, as described later to the system of all heat-treated etc.
The condition of making is worked hard, and controls the number density of the compound containing Sn of specific composition and size, control the solid solution of contained Sn with
The balance of precipitation, and also assure the solid solution capacity of Sn.Moreover, play the capture of the atomic vacancy of solid solution Sn, releasing effect, by depositing
In effect caused by the Sn compounds of above-mentioned specific composition and size, inhibit timeliness, realize the raising of formability, BH.
That is, as the characteristic after the room-temperature aging of manufactured plate, to automobile outer panels it is stamping when bending (before baking application)
It is 110MPa hereinafter, crimping processability is in embodiment 2.0 according to aftermentioned benchmark hereinafter, and automobile outer panels to take intensity
It is more than 100MPa that artificial age-hardening under the conditions of the baking application of 185 DEG C × 20 minutes, which measures (BH),.
On the other hand, in the present invention, in order to improve filiform corrosion resistance, so that the Snization of above-mentioned specific composition and size
The mode of the interface of conjunction object and aluminium base change more (elongated) is precipitated or crystallization.Thus, it is possible to make not contain the compound and base of Sn
The interface of material tails off and (shortens), can provide 6000 line aluminium alloys for having both formability, BH and good filiform corrosion resistance
Plate.
Specific embodiment
Hereinafter, embodiments of the present invention are specifically described according to important document.
(chemical composition composition)
First, to the chemical composition composition of the Al-Mg-Si systems of the present invention (following also referred to as 6000 systems) aluminium alloy plate such as
It illustrates lowerly.The 6000 line aluminium alloy plate of object of the present invention is requested to have as the plate of the outer panels of automobile
State many characteristics such as the excellent formability after room-temperature aging, BH, filiform corrosion resistance.
As in order to meet the characteristic of the plate needed for such requirement, by 30 days room temperatures after just T6 etc. is quenched after plate manufacture
For characteristic after timeliness, preferably：To automobile outer panels it is stamping when (baking application before) yield strength be 110MPa
Hereinafter, crimping processability in embodiment according to aftermentioned benchmark be 2.0 hereinafter, and automobile outer panels at 185 DEG C × 20 points
It is more than 100MPa that artificial age-hardening under the conditions of the baking application of clock, which measures (BH),.
As for meeting the condition from alloy composition side of such preferred plate characteristic, the alloy of aluminium alloy plate forms
Include Mg respectively in 6000 systems and in terms of quality %：0.3~1.0%, Si：0.5~1.5%, Sn：0.005~
0.2%th, Fe：0.02~1.0% and Mn：0.02~0.6% and the specific composition that is made of Al and inevitable impurity of surplus.
It is explained, the % statements of the content of each element refer to gross mass %.In addition, in the description, the percentage on the basis of quality
Rate (quality %) is identical with the percentage (weight %) on the basis of weight.In addition, the content about each chemical composition, sometimes will
" below X% (still, not including 0%) " it is expressed as " more than 0% and below X% ".
Here, in above-mentioned alloy composition, preferably BH more preferably, the mass ratio Si/Mg of Si and Mg it is such for more than 1
6000 line aluminium alloy plates of excessive Si types.
The other elements in addition to Mg, Si, Sn, Fe, Mn as above-mentioned alloy composition for inevitable impurity, be according to
According to the content (tolerance) of each element level of AA or even JIS specifications etc..That is, from the viewpoint of resource recycling, in this hair
In bright, as the melting raw material of alloy, not using only high-purity Al ingots, and it is a large amount of the use of 6000 is alloy, other aluminium
In the case of alloyed scrap material, low-purity Al ingots etc., its in addition to Mg, Si, Sn, Fe, Mn will necessarily be mixed into real mass
His element.Moreover, reduce the refining cost increase of these elements itself, need that the object of the invention, effect is not being hindered to contain
Range allow it is a degree of containing.
Specifically, in terms of quality %, can contain selected from Cr：Less than 0.4% (but not including 0%), Zr：0.3% with
Under (but do not include 0%), V：Less than 0.3% (but not including 0%), Ti：Less than 0.1% (but not including 0%), Cu：0.4% with
Under (but do not include 0%), Ag：Less than 0.2% (but not including 0%) and Zn：One kind in less than 1.0% (but not including 0%)
It is or two or more.
Hereinafter, each element in above-mentioned 6000 line aluminium alloy is carried out successively containing range and meaning or allowance
Explanation.
Si：0.5~1.5%
Si be solution strengthening and coating baking processing when artificial aging processing when helped to be formed as essential element
Age hardening capability is played in the Mg-Si systems precipitate that intensity improves and be for obtaining the outer panels institute as automobile
Need intensity (yield strength) and necessary element.It is in addition, excellent in order to be played in the coating baking processing after panel is configured to
Different age hardening capability, preferably Si/Mg mass ratioes are more than 1.0, make in Mg compared with general described excessive Si types
The more excessively 6000 line aluminium alloys composition containing Si.If Si contents are very few, the production quantity of Mg-Si systems precipitate is insufficient, because
This BH is significantly reduced.
On the other hand, if Si contents are excessive, coarse crystal and precipitate are formed in crystal grain and in crystal boundary, bending
Processability and filiform corrosion significantly reduce.Therefore, Si is 0.5~1.5% range.Preferred lower limiting value is 0.6%, more
Preferred upper limit value is 1.4%.
Mg：0.3~1.0%
Mg is also to be helped in solution strengthening and coating baking processing when artificial agings are handled as essential element to be formed
Age hardening capability is played in the Mg-Si systems precipitate that intensity improves and be for obtaining as the surrender needed for panel
Intensity and necessary element.If Mg contents are very few, the production quantity of Mg-Si systems precipitate is insufficient, therefore BH is significantly reduced.
Therefore, it is impossible to it obtains as the yield strength needed for panel.On the other hand, if Mg contents are excessive, coarse crystal is formed
And precipitate, bendability significantly reduce.Therefore, the content of Mg is 0.3~1.0% range.Preferred lower limiting value is
0.4%, preferred upper limit value is 0.8%.
Fe：0.02~1.0%
Fe is in all heat-treated and generates this together with specific number density with Al, others Si, Mn, Sn etc. during hot rolling
The essential elements of the compound of specific dimensions containing Sn specified in invention.If its content is very few, the above-mentioned spy containing Sn
The production quantity of fixed compound becomes very few, and the interface of above-mentioned specific compound and base material containing Sn tails off and (shortens), carries
High Filamentous tarnish resistance effect becomes smaller.On the other hand, it is above-mentioned specific containing Sn in crystal grain and in crystal boundary if Fe contents are excessive
The production quantity of compound become excessive, the formabilities such as crimping processability and filiform corrosion is made to be deteriorated.
Mn：0.02~0.6%
It is close specifically to count together with Al, others Si, Fe, Sn etc. when Mn and Fe is also in all heat-treated and during hot rolling
The essential elements of the compound of certain size containing Sn specified in the degree generation present invention.If its content is very few, contain
The production quantity of the above-mentioned specific compound of Sn becomes very few, and the interface of above-mentioned specific compound and base material containing Sn tails off
(shortening), the effect for improving filiform corrosion become smaller.On the other hand, if Mn contents are excessive, contain Sn in crystal grain and in crystal boundary
The production quantity of above-mentioned specific compound become excessive, the formabilities such as crimping processability and filiform corrosion is made to be deteriorated.
Sn：0.005~0.2%
Sn is necessary element, is had the following effects that：In the state of solid solution, by capturing atom sky at room temperature
Cave, so as to inhibit the diffusion of Mg, Si at room temperature, the long-term intensity inhibited at room temperature increases (room-temperature aging), during the room temperature
Plate stamping and forming after effect improves press formability, especially crimping processability when being panel.Moreover, on the other hand, due to
The coating baking processing of panel formed thereby can discharge captured hole when artificial agings handles, thus instead promotion Mg or
The diffusion of Si can improve BH.
The effect of these Sn is initially played by being dissolved Sn.If the content of Sn is very few, the solid solution capacity of Sn is reduced, it is impossible to
Fully capture hole can not play the room-temperature aging inhibition of above-mentioned Sn.As a result：It can inhibit the intensity increasing in room temperature
Add, yield strength increases, and not only crimping processability is deteriorated, and the production quantity of Mg-Si systems precipitate when BH is handled also is reduced, BH
Property is easily lower.
In the present invention, in addition to the Sn of above-mentioned solid solution, on the other hand, make a certain amount of Sn with the compound containing Sn
Form is precipitated or crystallization, so as to improve filiform corrosion resistance.But if the content of Sn is very few, the compound containing Sn also subtracts
It is few.
Therefore, in the compound containing Mn and Fe, the content of Sn is more than 1.0 mass % and equivalent circle diameter is 0.3
The average number density of the compound of~20 μm of range is insufficient.As a result：The length at the interface of these compounds and aluminium base
Also it is insufficient, filiform corrosion resistance can not be improved.
But even if the content of Sn is excessive, there is also boundaries for the solid solution capacity of Sn, increase solid solution capacity.If in addition, Sn
Content it is excessive, then Sn is in cyrystal boundary segregation, the reason of becoming grain-boundary crack, easily generates and splits in the hot rolling of the manufacturing process of plate
Line.
Therefore, the content of Sn is 0.005~0.2% range.Preferred lower limiting value is 0.01%, the preferred upper limit
Be worth is 0.18%.
(tissue)
Then, the tissue of the 6000 line aluminium alloy plates of the present invention is carried out as described below.
Sn compounds：
In the present invention, the tissue as the plate after manufacture (after quenched), is measured, and be defined as using 500 times of SEM
Composition identified using X-ray spectrum device, specific and the average number density of Sn compounds of size and the boundary of aluminium base
The number in face.
The compound of the specific composition and the Sn of size are containing both Mn and Fe or containing any in Mn or Fe
Person, Sn content be the Sn compounds (change containing Sn for the range that more than 1.0 mass % and equivalent circle diameter is 0.3~20 μm
Close object).
The average number density for meeting such defined Sn compounds is 500~3000/mm2Range, preferably 500~
2000/mm2Range, with ensure for play solid solution Sn above-mentioned room-temperature aging inhibition needed for Sn solid solution capacity.
In addition, the length for meeting the interface of such defined Sn compounds and aluminium base is removed with the overall circumference of the Sn compounds
The value obtained by measure area by above-mentioned SEM come in terms of 3~20/mm of average out to range, be preferably on average the range of 3~10/mm.
In this way, being precipitated in a manner of becoming more by the interface for making the aluminium base of the Sn compounds of above-mentioned specific composition and size or brilliant
Change, reduce the compound for not containing Sn of filiform corrosion resistance and the interface of base material so as to reduce, improve filiform corrosion resistance.
The average number density of Sn compounds：
It is more than 3000/mm in the average number density of above-mentioned specific composition and the Sn compounds of size2And excessive feelings
Under condition, the solid solution capacity of Sn is reduced, and can not play the room-temperature aging inhibition of above-mentioned Sn.As a result：It can inhibit in room temperature
Intensity increase, yield strength increases, and not only crimping processability is deteriorated, the production quantity of Mg-Si systems precipitate during BH processing
It reduces, BH is easily lower.
Its another aspect, in of the invention, in order to improve filiform corrosion resistance, and so that the interface of the Sn compounds and base material
Becoming the mode of more (elongated) makes Sn be precipitated to a certain extent in the form of specifically forming the compound with size or crystallization.
The inventors of the present invention study the addition of Sn and the relationship of filiform corrosion resistance.Its result is understood：In Al-
In the tissue of Mg-Si line aluminium alloy plates, based on certain manufacturing condition, the Sn added is entered in coarse compound, and is produced
It is raw be not easy as filiform corrosion starting point this it is special the phenomenon that.
Here, coarse compound be the Al-Fe systems generated in casting, soaking, hot rolling treatment, Al-Fe-Mn systems,
Al-Fe-Si systems, the intermetallic compound of Al-Fe-Mn-Si systems, refer to equivalent circle diameter be several μm~tens of μm compared with
Big intermetallic compound.If these coarse compounds are present in aluminium alloy, current potential than surrounding aluminium higher, as so-called
Cathode site plays a role.
Therefore, in these coarse compounds and the interface of aluminum mother plate, larger potential difference is generated, is very easy in corrosion
The state of aggravation.Such corrosion phenomenon is covered as above-mentioned car panel on aluminium alloy plate (panel) surface by resin involucra
In the state of embodied in the form of filiform corrosion (filiform stretch rust).
In this regard, by the way that above-mentioned coarse compound is made to contain Sn, so as to which the potential difference with the aluminium of surrounding becomes smaller, it is not easy as the moon
Pole site plays a role, and is not easy the starting point as filiform corrosion.That is, by making the length at the interface of Sn compounds and aluminium base be
Certain above range, and the interface of the compound for not containing Sn for reducing filiform corrosion resistance and base material is reduced, so as to
To improve filiform corrosion.
Formability, BH and good filiform corrosion resistance are had both as a result,.
Therefore, the regulation of above-mentioned specific composition and the average number density of the Sn compounds of size be also make Sn be only precipitated or
Crystallization a certain amount of (certain number density and certain perimeter) and the amount of precipitation of Sn or the benchmark of crystallization amount for improving filiform corrosion resistance.
Above-mentioned specific Sn compounds average number density less than 500/mm2And it is very few in the case of, can not obtain containing Mn and
The above-mentioned specific Sn compounds of Fe in itself, can not improve filiform corrosion resistance.
Sn compounds containing Mn and Fe：
Sn forms above-mentioned specific composition and size in the alloy composition of above-mentioned plate together with Mn and Fe contained by it
Sn compounds, if therefore plate do not contain these Mn and Fe, the Sn compounds of above-mentioned specific composition and size are inherently not
It can generate.But as long as Mn and Fe in the Sn compounds are deposited with the level (range) that aftermentioned EDX can be utilized to be detected
Without the content in Sn compounds to be carried out to quantitative provide respectively.
The Sn contents and size of Sn compounds：
In addition, in Sn compounds, the Sn contents compound very few less than 1.0 mass % and Sn or equivalent circle diameter
Even if less than several interfaces for meeting above-mentioned average number density or above compound of 0.3 μm of too small compound number and
In the presence of will not ensure the solid solution capacity of Sn.Moreover, the effect for improving above-mentioned formability, BH, filiform corrosion resistance etc. is small.
Therefore, these compounds are excluded from the Sn compounds of above-mentioned specific composition and size.
The upper limit of the Sn contents of the specific Sn compounds is simultaneously not specially provided, but upper limit value from manufacture gauge for
10 mass % or so.In addition, the equivalent circle diameter if the specific Sn compounds is more than coarse compound as 20 μm, then
The reason of as crackle, easily cracks in the hot rolling of the manufacturing process of plate etc..
The length (how many) at the interface of Sn compounds：
As the existence in above-mentioned specific composition and the plate tissue of the Sn compounds of size, if these is made to contain Snization
The interface for closing object and base material is elongated (becoming more), then filiform corrosion resistance improves.In these compounds containing Sn and the interface mistake of base material
In the case of few, the effect for improving filiform corrosion resistance becomes smaller.That is, these Sn compounds and the interface of aluminium base length with
The overall circumference (perimeter of all Sn compounds of above-mentioned specific composition and size total) of these compounds divided by above-mentioned SEM
Measure area obtained by value come in the case of counting less than 3/mm, the interface of Sn compounds and base material shortens.Therefore, resistance to silk is reduced
The interface of the tarnish resistance compound for not containing Sn of shape and base material is elongated (becoming more), and the effect for improving filiform corrosion resistance becomes smaller.
On the other hand, excessive if the interface of these Sn compounds and base material is more than 20/mm, the number of the compound containing Sn is close
Degree becomes more, and solid solution Sn amounts reduce, and can not obtain low yield strength and high BH.Therefore, the interface of compound containing Sn and base material with
Value obtained by the measure area of the overall circumference of these compounds divided by above-mentioned SEM counts 3~20/mm of average out to.It is more preferably average
Range for 3~10/mm.
The measure of Sn compounds：
Equivalent circle diameter is 0.3~20 μm of range, the Sn containing more than 1.0 mass % and contains both Mn's and Fe
The measure of the number density of compound utilizes 500 times of SEM (scanning electron microscope, Scanning Electron
Microscope it) carries out.Moreover, the Sn compounds of these specific compositions and size are filled using X-ray spectrum subsidiary SEM
It puts to identify, and less than 1.0 mass % or does not contain the compound of Mn or Fe with the content of Sn and mutually distinguish.In addition, it utilizes
Above-mentioned SEM can also distinguish between the compound for the size for being unsatisfactory for above range.
Using above-mentioned SEM measure to from for test plate (panel) surface 1/4, plate thickness direction arbitrary 10 positions point
(10 samples of acquisition) are carried out, the number density of the above-mentioned specific composition of these each samples and the Sn compounds of size is equalized
And obtain average number density (a/mm2).Specifically, to the right-angle cross-section in the plate thickness direction for test plate (panel) after firm modifier treatment,
By the arbitrary point in 1/4, the plate thickness direction from surface, pair face parallel with plate surface is surveyed using 500 times of SEM
It is fixed.About sample, 10 samples are extracted from above-mentioned position, mechanical lapping is carried out to plate cross-section samples surface, utilizes mechanical lapping
The about 0.25mm from plate surface is ground off, then is polished grinding, prepares the sample after being adjusted to surface.Then, the anti-of SEM is utilized
Radio subgraph measures the number of the compound of above-mentioned equivalent circle diameter range using automatic analyzer, calculates number density.It surveys
Position is determined for buck surface, and the mensuration region of every 1 sample is 180 μm of 240 μ m.
X-ray spectrum device is taken as energy dispersion type x-ray spectrometry (Energy Dispersive X-ray
Spectroscopy analytical equipment) is known, commonly referred to as EDX, and is attached to above-mentioned SEM, to above-mentioned equivalent circle diameter model
The composition for the compound enclosed carries out quantitative analysis.Moreover, when measuring the number of compound of above-mentioned equivalent circle diameter range, root
According to the content of Sn and whether substantially containing Mn and Fe, mutually distinguished with other compounds.Only identify it is above-mentioned it is specific composition and
The Sn compounds of size.In the present invention, also it can not detect Mn's or Fe in compound even with X-ray spectrum device
In the case of, it is similary less than the situation of 1.0 mass % with the content of Sn, regard as and above-mentioned spy as the compound without Mn or Fe
Fixed composition other compounds different with the Sn compounds of size.
And then the parsing of the reflected electron image by above-mentioned SEM, acquire above-mentioned specific composition and the Sn compounds of size
Overall circumference (mm), the length (/mm) at the interface of the Sn compounds and aluminium base is with by the measure of the overall circumference divided by above-mentioned SEM
Area (the field area of SEM：240 μ m is scaled mm for 180 μm2) obtained by value (mm/mm2) come count carry out said sample number
Be averaged acquire.
With the difference of the prior art：
In this way, in terms of the solid solution condition of Sn and with making the side that the solid solution condition is precipitated or the Sn compounds of crystallization balance
Face, the 6000 line aluminium alloy plates of the invention containing Sn are aluminium with 6000 of similary (same amount) containing Sn organizationally or in characteristic
Alloy sheets are different.That is, if the manufacturing condition of all heat-treated etc. is different, the solid solution capacity of Sn, the compound of Sn above-mentioned composition, number
Density and existing forms is waited also to differ widely with the how much of the interface of above-mentioned base material.
In other words, under the manufacturing condition (well-established law) of common plate, Sn is easily precipitated in the form of compound, and solid solution capacity is shown
It writes low (few).In addition, the above-mentioned composition of the compound of Sn, number density are also different, and also tail off with the interface of above-mentioned base material.Cause
This, even if similary (same amount) contains Sn, may not also become have as in the present invention with high level inhibit room-temperature aging and
Improve BH, crimping processability effect tissue and obtain the tissue of excellent filiform corrosion resistance.
By the way, the 6000 line aluminium alloy plates of previous addition Sn cannot give full play to the effect of such Sn.It is managed
By being speculated as：The previous solid solution or precipitation for being usually conceived to Mg, Si as essential element, but for being only adding for selectivity
The solid solution of the Sn of one of added elements, the existing forms being precipitated simultaneously less are paid close attention to.In addition, using conventional method manufacture it is plate,
The form that is primarily present of Sn is with the crystallization of compound form or precipitation (being hereinafter also referred to as precipitated).Unlike this, also speculate
Itself reason for this is that：Make Sn solid solutions more difficult in itself, the solid solution condition of Sn is extremely rare existing forms, therefore be not easy to by Sn's
The played effect of solid solution is had gained some understanding.
(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 manufactures work
Sequence is conventional method or well known method in itself, is tied to form the aluminium alloy ingot bar being grouped as to above-mentioned 6000 after casting and carries out homogeneous
Change heat treatment, implement hot rolling, cold rolling and as set plate thickness, then implement the modifier treatment such as solution hardening and manufacture.
But in these manufacturing processes, as the tissue of the plate of (quenched after) after manufacture, in order to make above-mentioned specifically to contain
Sn is formed and the average number density of the Sn compounds of size is is dissolved Sn and makes the solid solution of Sn flat with being precipitated in prescribed limit
Weighing apparatus, as described later, it is specified that the intermediate annealing in cold rolling way also becomes preferred in addition to average cooling rate when casting is controlled
Condition.If not such intermediate annealing condition is then difficult to be dissolved Sn.
And then in addition to this, the tissue as the plate of (quenched after) after manufacture, in order to make it is above-mentioned specifically containing Sn compositions and
The Sn compounds of size and the interface of aluminium base number in prescribed limit, all heat-treated is according to 2 stages under specified conditions
All heat-treated carry out.
Melting, casting cooling speed：
First, it is logical suitable for selection continuous casting process, semi-continuous casting method (DC castings) etc. in melting, casting process
Normal melting and casting method casts the molten aluminium alloy for being smelted and being adjusted in above-mentioned 6000 set member compositing range.Here, it is
As defined of the present invention it is dissolved Sn, and it is preferred that average cooling rate when making casting is from liquidus temperature to solidus
Temperature increases (quickening) to 30 DEG C/min or more as far as possible.
During temperature (cooling velocity) of high-temperature area when without such casting, the cooling speed of the high-temperature area
Degree is inevitable slack-off.When the average cooling rate of high-temperature area like this is slow, the temperature range of the high-temperature area it is coarse it is raw
Into crystal quantitative change it is more, the deviation of the plate width direction of ingot bar, the size of the crystal of thickness direction and amount also becomes larger.It is tied
Fruit is：It is increased in the possibility that the prescribed limit of the present invention can not be dissolved Sn.
Homogenize heat treatment：
Then, implement the heat treatment that homogenizes before to the aluminium alloy ingot bar hot rolling after above-mentioned casting.This homogenizes at heat
For the purpose of segregation in crystal grain of the reason (all heat-treated) by the homogenizing of tissue, i.e. in elimination ingot bar tissue.
But in the present invention, as being carried out after above-mentioned modifier treatment after room-temperature aging, (quenched after) after manufacture
The tissue of plate, in order to make above-mentioned specific composition and the interface of the Sn compounds of size and aluminium base number for prescribed limit
It is interior, carry out all heat-treated according to following specified conditions.
1st stage of all heat-treated 400~500 DEG C range keep 1~10 hour.Make above-mentioned specific group as a result,
Into with the dispersion of the Sn compound fines of size, and make the number density of the compound and the interface of aluminium base number for above-mentioned rule
Determine in range.If the soaking temperature is less than 400 DEG C or the retention time was less than 1 hour, make above-mentioned specifically containing Sn compositions and ruler
The interface of very little Sn compound fines dispersion, Sn compounds and aluminium base number with the overall circumference of these compounds divided by above-mentioned
Value obtained by the measure area of SEM is difficult to reach more than average out to 3/mm to count.If in addition, the retention time in the 1st stage surpasses
10 hours are spent, then the number density of the Sn compounds of above-mentioned specific composition and size is more than 3000/mm2And it is excessive, inhibit room
The solid solution capacity of Sn needed for warm hardening is insufficient.
Then, all heat-treated in the 2nd stage further heated is kept for 3 hours or more in 520~560 DEG C of range.
In all heat-treated in the 2nd stage, make the compound solid solution with Mg-Si-Sn systems existing for ingot casting crystalline form, and make
Being dissolved Sn amounts increases.If the temperature of all heat-treated in the 2nd stage is less than 520 DEG C or the retention time was less than 3 hours, with ingot casting
The solid solution of the compound of Mg-Si-Sn systems is insufficient existing for crystalline form, inhibits the solid solution capacity of the Sn needed for room-temperature aging
It is insufficient.On the other hand, if the soaking temperature in the 2nd stage is more than 560 DEG C, ingot casting melting loss.In addition, the holding in the 2nd stage
Time can be longer, but in terms of production efficiency, economy, nothing requires more than 20 hours.
If the retention time that can make 400 DEG C~500 DEG C of temperature region is 1~10 hour, embodiment institute as be described hereinafter
Show, as all heat-treated in 2 stages, can be kept at a certain temperature, or pass through heating, Slow cooling etc.
And change the heat treatment of temperature successively.In short, temperature change continuously occurs even with heating, Slow cooling etc., as long as
It is kept for 1 hour or more and less than 10 hours in 400~500 DEG C of temperature regions.
Hot rolling：
Hot rolling is made of according to the plate thickness of rolling the roughing operation and finish to gauge process of ingot bar (slab).In these roughing works
In sequence and finish to gauge process, suitable for using the milling train of reversible or tandem etc..
At this moment, under conditions of hot rolling (roughing) start temperature is more than solidus temperature, it may occur that burning, therefore hot rolling sheet
Body is difficult to.In addition, when hot rolling start temperature is less than 350 DEG C, load during hot rolling is excessively high, and hot rolling is difficult in itself.
Therefore, hot rolling start temperature is preferably 350 DEG C~solidus temperature, the range of more preferably 400 DEG C~solidus temperature.
The annealing of hot rolled plate：
The annealing (black annealing) before the cold rolling for carrying out the hot rolled plate is not necessarily required, but in order to pass through the miniaturization sum aggregate of crystal grain
The optimization knitted is combined to further improve the characteristics such as formability, the annealing before the cold rolling of the hot rolled plate can also be implemented.
Cold rolling：
It in cold rolling, rolls above-mentioned hot rolled plate, is fabricated to the cold-reduced sheet of desired final plate thickness (also including coiled material).But
Be, in order to make the further miniaturization of crystal grain, it is expected no matter road number why and make total cold rolling rate be more than 60%.
Intermediate annealing：
Preferably：Before the cold rolling (after hot rolling) or in the way of cold rolling (between passage), by plate in 480 DEG C or more and fusing point
Following high temperature is kept for 0.1~10 second, then, carries out forcing cooling (chilling) to room with 3 DEG C/sec or more of average cooling rate
The intermediate annealing of temperature makes to use this Sn solid solution generated with compound form for hot-rolled process extremely etc..Using conventional method,
Sn is easily precipitated, once the Sn being precipitated is difficult to be dissolved once again, in order to be dissolved Sn as defined of the present invention, it is difficult to merely with
Aftermentioned solution treatment is dissolved Sn, needs to carry out the heat treatment of high temperature using intermediate annealing.
To the intermediate annealing condition, if the temperature of plate, less than 480 DEG C, the solid solution capacity of Sn is insufficient.If in addition, after annealing
The pressure that using air cooling, spraying, water cooling etc. is cooled to room temperature of the cooling not for 3 DEG C/sec or more of average cooling rate is cold
But (chilling), i.e. average cooling rate are less than 3 DEG C/sec, then once the Sn of solid solution can be precipitated and form compound again.
Annealing under the conditions of such further includes chilling, is difficult to accomplish using batch-type furnace, needs while by plate debatching into stove
The continuous heat treating furnace for leading to plate and being batched.
Solid solution and quenching treatment：
After cold rolling, solution hardening processing is carried out.About solution treatment and quenching treatment, common continuous heat can be used
Line is heated, is cooled down, and is not particularly limited.But due to it is expected to obtain the sufficient solid solution capacity of each element and making plate group
The crystal grain knitted is finer, and it is desirable to be heated to below 520 DEG C or more and melting temperature with 5 DEG C/sec or more of heating speed
Solid solution temperature and keep 0~10 second under conditions of carry out.Moreover, stop being averaged for temperature from solutionizing temperature to quenching
Cooling velocity is preferably 3 DEG C/sec or more.If the cooling velocity is small, the number density of above-mentioned Sn compounds becomes more, and solid solution Sn becomes
It is very few.Accordingly, it is difficult to 0.2% yield strength when meeting forming be below 110MPa low yield strength, crimping processability be
Less than the 2.0 and BH under conditions of 185 DEG C × 20 minutes is more than 100MPa.In addition, Mg-Si based compounds in cooling
It is precipitated Deng easy, the starting point of crackle when easily becoming stamping, bending machining, these formabilities reduce.In order to ensure this
Cooling velocity, quenching treatment selects to cool down using the forced airs such as fan respectively, spraying, water spray, impregnating magnetism servo-electric motor water-cooling and
Condition.
By the way, solution hardening processing, temperature of black annealing condition after above-mentioned hot rolling etc. also with above-mentioned centre
Annealing conditions are approximate, if being unsatisfactory for all many conditions such as above-mentioned 520 DEG C or more of temperature without above-mentioned intermediate annealing or progress,
The black annealing after the solution hardening processing, above-mentioned hot rolling is then only carried out, Sn can not be made only with above-mentioned aequum or above-mentioned specified amount
Solid solution.
Preliminary aging treatment (reheating processing)：
Quenching treatment is carried out after such solution treatment and after being cooled to room temperature, to the greatest extent may be used within 1 hour (60 minutes)
Preliminary aging treatment (reheating processing) is carried out to plate in time that can be short.
After quenching treatment until room temperature, if the room temperature until preliminary aging treatment starts (heating starts)
Retention time is long more than 1 hour, then room-temperature aging carries out and makes BH reductions.Therefore, the room temperature i time it is more short more
Good, solid solution and quenching treatment and reheating processing can also be taken and be carried out continuously almost without the mode of time difference, lower limit
Time does not set especially.
The temperature of the preliminary aging treatment and retention time be preferably 80~150 DEG C of temperature range keep 3 hours with
It is upper and less than 50 hours.At this point it is possible to the temperature holding at this 80~150 DEG C is set as keeping centainly in the temperature range
Temperature or the heat treatment for changing temperature successively by heating, slow cool down.In short, even with slow cool down or heating etc. continuously into
Trip temperature changes, as long as the temperature region at 80~150 DEG C is kept for 3 hours or more and less than 50 hours.Reheating processing
Afterwards to the cooling of room temperature, cooling body during above-mentioned quenching can also be used with natural cooling, and for the efficient activity of production
Carry out pressure chilling.
If giving standby ageing treatment not in these preferred condition and ranges, 0.2% of plate when car panel is shaped
Yield strength is reduced to 110MPa hereinafter, and being not easy that BH is made to be more than 100MPa.
Hereinafter, enumerating embodiment further illustrates the present invention, but the present invention is not limited certainly by following embodiments, in energy
Implementation can also suitably be changed in the range of the forward and backward objective stated by enough meeting, these are all contained in the technology model of the present invention
In enclosing.
Embodiment
Hereinafter, the embodiment of the present invention is illustrated.The difference according to above-mentioned all heat-treated condition, intermediate annealing condition
How much differences at the interface of the average number density amounts of the Sn compounds of above-mentioned composition and size, the Sn compounds and aluminium base made
6000 line aluminium alloy plates, after fabrication to the plate evaluate room temperature keep 30 days after intensity, BH (coating baking hardenings
Property), crimping processability, filiform corrosion resistance.The results are shown in Table 2 for it.
The specific manufacturing condition of these aluminium alloy plates is as follows.Commonly through each composition shown in DC casting meltings table 1
Aluminium alloy ingot bar.At this moment, each example jointly sets average cooling rate when casting from liquidus temperature to solidus temperature
It is 50 DEG C/min.It is explained, the content of each element in the table 1 for representing the composition of 6000 line aluminium alloy plates of each example
In display, using the numerical value of each element as the display of blank, its content is represented below detectable limit and for not comprising these yuan
The 0% of element.
After above-mentioned ingot casting is carried out all heat-treated under the conditions of each shown in table 2, opened at a temperature of each example in the 2nd stage
Begin hot roughing.Moreover, each example is immediately hot-rolled down to thickness 2.5mm using finish to gauge jointly, hot rolled plate is made.Each example jointly should
Hot rolled plate carries out utilizing continuous annealing furnace under various conditions (between passage) in the passage way of cold rolling according to such shown in table 2
Intermediate annealing is finally made the cold-reduced sheet (sheet) of thickness 1.0mm.
And then above-mentioned each cold-reduced sheet is carried out solution treatment by each example in 560 DEG C of niter oven jointly, reaches target
Kept for 10 seconds after temperature, using from solutionizing temperature to quenching stop temperature average cooling rate be 50 DEG C/sec water cooling into
Row quenching treatment.Carry out keeping the preliminary aging treatment of 5 hours after the firm quenching at 100 DEG C (with 0.6 DEG C/h after holding
Carry out Slow cooling).
From each plate cutting after these firm modifier treatment for test plate (panel) (blank), as each tissue for test plate (panel), measure above-mentioned
The interface of the average number density amount of Sn compounds of composition and size, the Sn compounds and aluminium base number.In addition, from upper
Each plate cutting after modifier treatment after being placed at room temperature for 30 days is stated for test plate (panel) (blank), and (AS is surrendered to each intensity for test plate (panel)
Intensity：Plate manufacture after carry out 0.2% yield strength after 30 days room-temperature agings) and BH investigated.Their result is such as
Shown in table 2.
(tissue for supplying test plate (panel))
Modifier treatment soon respectively in test plate (panel), compound containing Mn and Fe, the content of Sn for 1.0 mass % with
Upper and equivalent circle diameter is average number density (a/mm of the compound of 0.3~20 μm of range2) utilization use above-mentioned 500
Times SEM and the assay method of X-ray spectrum device acquire.In addition, using above-mentioned 500 times of SEM and X ray light is used
The assay method of spectral apparatus forms the length at the interface of the Sn compounds and aluminium base of above-mentioned composition and size and ruler with above-mentioned
The overall circumference (perimeter of all Sn compounds of above-mentioned composition and size total) of very little Sn compounds divided by the survey of above-mentioned SEM
The form for determining the value (/mm) obtained by area acquires.
(tensile test)
It is respectively each for test plate (panel) extraction after being placed at room temperature for 30 days after above-mentioned modifier treatment about above-mentioned tensile test
No. 5 test films (25mm × 50mmGL × plate thickness) of JISZ2201 carry out tension test in room temperature.Make the drawing of test film at this time
Stretch the right angle orientation that direction is rolling direction.Tensile speed is 5mm/ minutes before 0.2% yield strength is reached, strong in surrender
It is 20mm/ minutes below degree.The N numbers of the feature measurement of machinery are 5, with each mean value calculation.It is explained, after above-mentioned BH
The measuring test film of yield strength in, using the cupping machine to the test film imparting simulate the stamping of plate
After 2% prestrain, then carry out above-mentioned BH processing.
As after above-mentioned 30 days room-temperature agings shape when plate characteristic, by shown in table 2 As0.2% yield strengths (into
0.2% yield strength during shape) be below 110MPa, crimping processability is in embodiment less than 2 according to aftermentioned benchmark
The formability that situation is set as the former material plate of automobile outer panels is qualified.
(BH)
By it is each for test plate (panel) respectively jointly using above-mentioned tension test acquire its after the room-temperature aging of above-mentioned 30 days again into
0.2% yield strength for test plate (panel) after the row artificial age-hardening of 185 DEG C × 20 minutes processing (after BH) is (after BH
0.2% yield strength).Moreover, yield strength according to table 2 incrementss (0.2% yield strength after above-mentioned BH with it is upper
State the difference of As0.2% yield strengths), each BH for test plate (panel) is evaluated, is more than 100MPa by the incrementss of 0.2% yield strength
Situation be set as BH qualification.
(crimping processability)
Crimping processability after above-mentioned be placed at room temperature for 30 days for test plate (panel) only to respectively carrying out.Experiment uses the slat of 30mm wide
Test film after 90 ° of bending machinings of the interior bending R1.0mm formed by downward flange, carries out the inside of clamping 1.0mm thickness
Part, then by folded bent portion inwardly successively carry out folded bent to about 130 degree pre-curl process, folded bent 180 degree
And end is made to be processed with the flat crimping that inner part touches.The surface for visually observing the bending section (curved edge portion) of the flat crimping is thick
Surface state such as rough, the small generation of crackle, big crackle, and visual valuation is carried out according to following benchmark, and will be up to
Benchmark 0~2 is set as qualified.
0：Flawless, rough surface, 1：Slight rough surface, 2：The rough surface of severe, 3：Tiny area crackle, 4：
With linear continuous face crack, 5：Rupture
(filiform corrosion resistance)
To above-mentioned respectively being evaluated for the filiform corrosion resistance of test plate (panel) after room-temperature aging.About for evaluation
Test method, from the above-mentioned plate that 80 × 150mm is respectively cut for test plate (panel) after 3 days room-temperature agings, in the degreasing bath of sodium carbonate system
Middle dipping 40 DEG C × 2 minutes (and utilize the stirring of blender), to having carried out ungrease treatment for examination material surface.Then, exist
After impregnating 1 minute (carrying out the stirring using blender) in the zinc system surface adjustment bath of room temperature, 2 are impregnated in 35 DEG C of trbasic zinc phosphates are bathed
Minute, implement trbasic zinc phosphate processing, electrodeposition coating (20 μm of thickness) carried out according still further to the coating process of common member for automobile,
In the 185 DEG C of baking for carrying out 20 minutes processing.Later, film is made to bring the cross-cut flaw of length 50mm into, by brine spray
24 hours → moistening (85%, 40 DEG C of humidity) 120 hours → spontaneously dries (room temperature) 24 hours cycle and carries out 8 cycles, surveys
Determine length of the width of the unilateral rust in cross-cut portion as filiform corrosion.
About the evaluation of filiform corrosion resistance, commented with the maximum width of the unilateral rust in above-mentioned cross-cut portion
The situation of maximum short of width 1mm is evaluated as ◎, more than 1mm and the situation less than 2mm is evaluated as zero by valency, by 2mm with
The upper and situation less than 3mm is evaluated as △, the situation of the length of more than 3mm is evaluated ×, the situation of ◎ and zero is judged as resistance to
The excellent material of filiform corrosion (qualification).
Each example (conjunction of table 1 in present component compositing range shown in the number 1~3,9,12,14~21 of table 2
Golden designation 1~11) and including all heat-treated, intermediate annealing above-mentioned optimum condition in the range of manufacture.Therefore, as shown in table 2,
Above-mentioned each example meets the average number density of the Sn compounds of above-mentioned composition given to this invention and size, the Sn compounds
With the interface of aluminium base number, the solid solution of Sn obtains balance with precipitation.
As a result：As shown in table 2, in above-mentioned each example, even if after above-mentioned modifier treatment during the room temperature of 30 days
After effect, can also make to automobile outer panels it is stamping when (baking application before) As0.2% yield strengths for 110MPa with
Under, the evaluation of crimping processability is excellent and is 0~2 and automobile outer panels are under the conditions of the baking application of 185 DEG C × 20 minutes
It is more than 100MPa that artificial age-hardening, which measures (BH),.In addition, filiform corrosion resistance is also excellent.
On the other hand, as being known as table 2, although using the table 1 in present component compositing range
Alloy number 1,2,3 or 18,19 but all heat-treated condition or intermediate annealing condition be in comparative example 4~8 outside preferred scope,
10th, in 11,13,28,29, as shown in table 2, the average of the Sn compounds of above-mentioned composition and size is close specified in the present invention
Degree, the Sn compounds and aluminium base interface number any one of deviate and provide, do not obtain the solid solution and precipitation of Sn
Balance.
As a result：As shown in table 2 like that, in above-mentioned each comparative example, the room-temperature aging of 30 days after above-mentioned modifier treatment
Afterwards, to automobile outer panels it is stamping when, yield strength it is excessively high and too low and insufficient more than 110MPa or BH
100MPa or filiform corrosion resistance are poor.
In comparative example 4,6,13, the retention time of all heat-treated in the 1st stage is too short or is not carried out for the 1st stage
All heat-treated.Therefore, the average number density of the Sn compounds of above-mentioned composition and size is very few, and the interface of Sn compounds and base material is not
Sufficient 3/mm, filiform corrosion are poor.
In comparative example 5,7,10, the retention time of all heat-treated in the 1st stage is long or the soaking in the 2nd stage at
It is too low to manage temperature.Therefore, Sn compounds are excessive, can not substantially ensure solid solution Sn, therefore AS yield strengths are high, yield strength increases
Amount is also low.In addition, intermediate annealing is also not carried out in comparative example 7, in comparative example 10, cooling velocity after intermediate annealing also mistake
It is low.
In comparative example 8,11, intermediate anneal temperature is too low.Therefore, Sn compounds are excessive, can not substantially ensure solid solution Sn,
Therefore AS yield strengths are excessively high, and yield strength incrementss are also low.
In comparative example 28,29, although using the alloy number 18,19 of the table 1 in present component compositing range,
Intermediate anneal temperature is not imposed, and the cooling velocity after intermediate annealing is too low.Therefore, Sn compounds are excessive, can not substantially ensure solid
Molten Sn, therefore AS yield strengths are excessively high, yield strength incrementss are also low.
In addition, in the comparative example 22~27,30~32 of table 2, although being manufactured in above-mentioned preferred condition and range,
It is the alloy number 12~17,20~22 using table 1, it is necessary to which the respective content of any one of Mg, Si, Sn of element exist
Other than the scope of the invention.Therefore, in these comparative examples 22~27,30~32, as shown in table 2,30 days after above-mentioned modifier treatment
Room-temperature aging after it is stamping when yield strength it is excessively high and more than the too low and insufficient 100MPa of 110MPa or BH,
Or filiform corrosion resistance is poor.
Comparative example 22 is the alloy 12 of table 1, and Si is very few.
Comparative example 23 is the alloy 13 of table 1, and Si is excessive.
Comparative example 24 is the alloy 14 of table 1, and Sn is very few.
Comparative example 25 is the alloy 15 of table 1, and Sn contents are excessive.Therefore, it is cracked in hot rolling, hot rolled plate in itself can not
It is manufactured.
Comparative example 26 is the alloy 16 of table 1, and Fe is excessive.
Comparative example 27 is the alloy 17 of table 1, and Mn is excessive.
Comparative example 30 is the alloy 20 of table 1, and Fe, Mn are very few.
Comparative example 31 is the alloy 21 of table 1, and Mg is very few.
Comparative example 32 is the alloy 22 of table 1, and Mg is excessive.
According to the above embodiments as a result, for have both include Sn 6000 line aluminium alloy plates room-temperature aging after it is strong
Degree, formability especially crimping processability, BH, filiform corrosion resistance, it was confirmed that the present invention specified in composition, Sn solid solution with
Precipitation balances each other or the critical meaning or even effect of preferred manufacturing condition.
[table 1]
[table 2]
The present invention is described in detail by, but can be before the spirit and scope of the present invention are not departed from reference to specific mode
It puts and carries out various change and modification, this is self-evident to those skilled in the art.
It is explained, the application is based on Japanese patent application (Japanese Patent Application 2014- filed in August in 2014 27 days
173277) it, is had been incorporated entirely through reference.
Industrial availability
According to the present invention it is possible to provide the formability after disposing the room-temperature aging as automobile outer panels, BH will
Seek and also improve the 6000 line aluminium alloy plates containing Sn of filiform corrosion resistance.It is aluminium that its result, which can especially expand 6000,
Application of the alloy sheets in automobile outer panels.
Claims (2)
1. a kind of aluminium alloy plate, which is characterized in that it is by Mg in terms of quality %：0.3~1.0%, Si：0.5~1.5%, Sn：
0.005~0.2%, Fe：0.02~1.0%, Mn：0.02~0.6%, surplus：The Al- that Al and inevitable impurity are formed
Mg-Si line aluminium alloy plates, wherein,
It as the tissue of the aluminium alloy plate, is measured using 500 times of SEM, in the change identified using X-ray spectrum device
It closes in object, the content containing Mn and Fe, and Sn is the Sn for the range that more than 1.0 mass % and equivalent circle diameter is 0.3~20 μm
The average number density of compound is 500~3000/mm2Range, and the length at the interface of the Sn compounds and aluminium base
Degree calculates the model of 3~20/mm of average out to value obtained by the measure area of the overall circumference of the Sn compounds divided by the SEM
It encloses.
2. aluminium alloy plate according to claim 1, wherein, also contained selected from Cr in terms of quality %：More than 0% and 0.4%
Below, Zr：More than 0% and less than 0.3%, V：More than 0% and less than 0.3%, Ti：More than 0% and less than 0.1%, Cu：It is more than
0% and less than 0.4%, Ag：More than 0% and less than 0.2% and Zn：More than 0% and one or both of less than 1.0% with
On.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014173277A JP6315582B2 (en) | 2014-08-27 | 2014-08-27 | Aluminum alloy sheet for forming |
| JP2014-173277 | 2014-08-27 | ||
| PCT/JP2015/074304 WO2016031941A1 (en) | 2014-08-27 | 2015-08-27 | Aluminum alloy sheet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN106661680A CN106661680A (en) | 2017-05-10 |
| CN106661680B true CN106661680B (en) | 2018-06-29 |
Family
ID=55399824
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201580043382.9A Expired - Fee Related CN106661680B (en) | 2014-08-27 | 2015-08-27 | Aluminium alloy plate |
Country Status (5)
| Country | Link |
|---|---|
| US (1) | US20170349978A1 (en) |
| JP (1) | JP6315582B2 (en) |
| KR (2) | KR20170038857A (en) |
| CN (1) | CN106661680B (en) |
| WO (1) | WO2016031941A1 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP3362581B1 (en) * | 2015-10-14 | 2022-09-14 | Nanoal LLC | Aluminum-iron-zirconium alloys |
| CN107058815B (en) * | 2016-12-29 | 2019-02-12 | 苏州中色研达金属技术有限公司 | 3C Product appearance member 6xxx line aluminium alloy and its processing method |
| CN111254324A (en) * | 2018-11-30 | 2020-06-09 | 宝山钢铁股份有限公司 | Al-Mg-Si alloy plate and manufacturing method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0616044A2 (en) * | 1993-03-03 | 1994-09-21 | Nkk Corporation | Method of manufacturing natural aging retardated aluminum alloy sheet |
| CN1160772A (en) * | 1996-01-05 | 1997-10-01 | 株式会社神户制钢所 | Aluminum alloy sheet for lithographic printing plates and method for manufacturing the same |
Family Cites Families (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06340940A (en) * | 1993-06-02 | 1994-12-13 | Kobe Steel Ltd | Aluminum alloy sheet excellent in press formability and baking hardenability and its production |
| JPH0860314A (en) * | 1994-08-17 | 1996-03-05 | Sky Alum Co Ltd | Production of aluminum alloy sheet for forming |
| JPH09249950A (en) * | 1996-03-15 | 1997-09-22 | Nippon Steel Corp | Production of aluminum alloy sheet excellent in formability and hardenability in coating/baking |
| JPH10219382A (en) * | 1997-02-04 | 1998-08-18 | Nippon Steel Corp | Aluminum alloy sheet excellent in formability/ workability and coating/baking hardenability and its production |
| JPH10226894A (en) | 1997-02-17 | 1998-08-25 | Nippon Steel Corp | Production of aluminum alloy sheet excellent in formability, baking finish hardenability, chemical convertibility and corrosion resistance |
| 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 |
| JP5278494B2 (en) * | 2004-01-07 | 2013-09-04 | 新日鐵住金株式会社 | Method for producing 6000 series aluminum alloy plate excellent in paint bake hardenability |
-
2014
- 2014-08-27 JP JP2014173277A patent/JP6315582B2/en active Active
-
2015
- 2015-08-27 US US15/506,595 patent/US20170349978A1/en not_active Abandoned
- 2015-08-27 CN CN201580043382.9A patent/CN106661680B/en not_active Expired - Fee Related
- 2015-08-27 WO PCT/JP2015/074304 patent/WO2016031941A1/en active Application Filing
- 2015-08-27 KR KR1020177005023A patent/KR20170038857A/en active IP Right Grant
- 2015-08-27 KR KR1020187023407A patent/KR20180095116A/en active Application Filing
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| EP0616044A2 (en) * | 1993-03-03 | 1994-09-21 | Nkk Corporation | Method of manufacturing natural aging retardated aluminum alloy sheet |
| CN1160772A (en) * | 1996-01-05 | 1997-10-01 | 株式会社神户制钢所 | Aluminum alloy sheet for lithographic printing plates and method for manufacturing the same |
Also Published As
| Publication number | Publication date |
|---|---|
| US20170349978A1 (en) | 2017-12-07 |
| JP2016047948A (en) | 2016-04-07 |
| KR20170038857A (en) | 2017-04-07 |
| KR20180095116A (en) | 2018-08-24 |
| WO2016031941A1 (en) | 2016-03-03 |
| CN106661680A (en) | 2017-05-10 |
| JP6315582B2 (en) | 2018-04-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5203772B2 (en) | Aluminum alloy sheet excellent in paint bake hardenability and suppressing room temperature aging and method for producing the same | |
| KR101667504B1 (en) | Aluminum alloy plate exhibiting excellent baking finish hardening properties | |
| JP5746528B2 (en) | Aluminum alloy sheet with excellent bake hardenability | |
| KR101850234B1 (en) | Aluminum alloy plate having excellent moldability and bake finish hardening properties | |
| KR101407751B1 (en) | Alluminum alloy sheet superior in baking paint hardenability | |
| KR20140114031A (en) | Aluminum alloy sheet with excellent baking-paint curability | |
| WO2014126073A1 (en) | Aluminum alloy sheet with excellent baking paint hardenability | |
| CN107109548A (en) | Aluminium alloy plate | |
| JP2017179468A (en) | Aluminum alloy sheet with high formability | |
| KR101802677B1 (en) | Aluminum alloy plate having excellent bake hardening properties | |
| JPWO2013015110A1 (en) | Aluminum alloy plate and method for producing aluminum alloy plate | |
| CN106574327A (en) | Aluminum alloy sheet for forming | |
| JP6506678B2 (en) | Aluminum alloy sheet for automobile structural member and method of manufacturing the same | |
| CN106574328B (en) | Aluminium alloy plate | |
| CN106661680B (en) | Aluminium alloy plate | |
| JP2009173973A (en) | Aluminum alloy sheet having excellent ridging mark property upon forming | |
| JP2017078211A (en) | Aluminum alloy sheet having high moldability | |
| JP6190308B2 (en) | Aluminum alloy sheet with excellent formability and bake hardenability | |
| JP4238019B2 (en) | Aluminum alloy panel for flat hem processing | |
| JP5918187B2 (en) | Aluminum alloy sheet with excellent bake hardenability | |
| JP6301175B2 (en) | Aluminum alloy sheet with excellent formability and bake hardenability | |
| JP6005613B2 (en) | Aluminum alloy sheet with excellent bake hardenability | |
| KR20220025670A (en) | Al-Mg-Si BASED ALUMINUM ALLOY SHEET HAVING EXCELLENT FORMABILITY | |
| JP5918186B2 (en) | Aluminum alloy sheet with excellent bake hardenability |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant | ||
| CF01 | Termination of patent right due to non-payment of annual fee | ||
| CF01 | Termination of patent right due to non-payment of annual fee |
Granted publication date: 20180629 Termination date: 20200827 |