CN1141958A - Method for production of aluminium alloy plate with good characteristics of shaping and thermo hardening - Google Patents
Method for production of aluminium alloy plate with good characteristics of shaping and thermo hardening Download PDFInfo
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- CN1141958A CN1141958A CN95107003A CN95107003A CN1141958A CN 1141958 A CN1141958 A CN 1141958A CN 95107003 A CN95107003 A CN 95107003A CN 95107003 A CN95107003 A CN 95107003A CN 1141958 A CN1141958 A CN 1141958A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 10
- 238000004519 manufacturing process Methods 0.000 title claims description 10
- 238000007493 shaping process Methods 0.000 title description 6
- 239000000463 material Substances 0.000 claims abstract description 45
- 238000010438 heat treatment Methods 0.000 claims abstract description 40
- 238000005096 rolling process Methods 0.000 claims abstract description 28
- 238000011282 treatment Methods 0.000 claims abstract description 27
- 150000001875 compounds Chemical class 0.000 claims abstract description 23
- 238000000034 method Methods 0.000 claims abstract description 22
- 230000032683 aging Effects 0.000 claims abstract description 21
- 238000005097 cold rolling Methods 0.000 claims abstract description 7
- 239000013078 crystal Substances 0.000 claims description 17
- 238000005098 hot rolling Methods 0.000 claims description 15
- 238000005266 casting Methods 0.000 claims description 10
- 239000000203 mixture Substances 0.000 claims description 5
- 238000000137 annealing Methods 0.000 claims description 4
- 239000012535 impurity Substances 0.000 claims description 4
- 238000007669 thermal treatment Methods 0.000 claims description 4
- 239000002001 electrolyte material Substances 0.000 claims description 2
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 abstract 1
- 239000004922 lacquer Substances 0.000 abstract 1
- 229910045601 alloy Inorganic materials 0.000 description 24
- 239000000956 alloy Substances 0.000 description 24
- 239000000243 solution Substances 0.000 description 23
- 238000009792 diffusion process Methods 0.000 description 17
- 230000000694 effects Effects 0.000 description 16
- 239000006104 solid solution Substances 0.000 description 16
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 11
- 230000000052 comparative effect Effects 0.000 description 10
- 238000001816 cooling Methods 0.000 description 7
- 229910018134 Al-Mg Inorganic materials 0.000 description 6
- 229910018467 Al—Mg Inorganic materials 0.000 description 6
- 230000006866 deterioration Effects 0.000 description 5
- 229910052782 aluminium Inorganic materials 0.000 description 4
- 239000004411 aluminium Substances 0.000 description 4
- 230000033228 biological regulation Effects 0.000 description 4
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 238000006243 chemical reaction Methods 0.000 description 3
- 238000004512 die casting Methods 0.000 description 3
- 239000002244 precipitate Substances 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 238000005275 alloying Methods 0.000 description 2
- 239000000470 constituent Substances 0.000 description 2
- 229910000765 intermetallic Inorganic materials 0.000 description 2
- 238000010791 quenching Methods 0.000 description 2
- 230000000171 quenching effect Effects 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 229910000952 Be alloy Inorganic materials 0.000 description 1
- 150000001398 aluminium Chemical class 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 230000003628 erosive effect Effects 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000446 fuel Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 239000010687 lubricating oil Substances 0.000 description 1
- 229910052748 manganese Inorganic materials 0.000 description 1
- 238000006386 neutralization reaction Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000004088 simulation Methods 0.000 description 1
- 238000003892 spreading Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
- 238000004381 surface treatment Methods 0.000 description 1
- 229920001187 thermosetting polymer Polymers 0.000 description 1
- 229910052719 titanium Inorganic materials 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 229910052720 vanadium Inorganic materials 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 230000037303 wrinkles Effects 0.000 description 1
- 229910052725 zinc Inorganic materials 0.000 description 1
- 229910052726 zirconium Inorganic materials 0.000 description 1
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
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
-
- 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
-
- 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
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
- B21B2003/001—Aluminium or its alloys
Abstract
The invention aims to improve the formability and the heating sclerosing performance of an aluminium alloy sheet. The aluminium alloy sheet is used as an automobile outer plate or a plate for a cartwheel and is painted with lacquer. The aluminium alloy sheet is formed through the following steps: heat an AL-Mg-Si alloy sheet to above 480 degrees, hot roll the sheet between 360 degrees and 450 degrees for less than 15 minutes and make the final temperature below 360 degrees after the rolling, after that conduct cold rolling process, then heat for 10 seconds to let the temperature rise to 450degrees for solution treatment; put the sheet under room temperature for natural aging for more than one hour, during which the conductivity is within 35-55%ACS, then process the sheet with heating treatment under the temperature of 180-300 degrees without reducing the conductivity for more than 10 seconds and less than 10 minutes. The average size of the grains on the parallel faces of the plate before the heat treatment and grains after the heat treatment is less than 90 microns, and the average ration of the rolling length to size of the grains at the vertical direction( the rolling to the vertical length) is 0.5-4; the biggest average length of the compound which contains Si in the material is less than 10 microns.
Description
The present invention relates to a kind of manufacture method of aluminium plate, this aluminium plate is at the member that is used for carrying out on parts, electric product, mechanical part etc. at the such automobile of the wheel of automobile, two-wheel car etc. and cover plate baking vanish after the processing that is shaped, particularly obtain a kind of have excellent moldability and when after shaping, carrying out baking vanish, the sheet material that enlarges markedly through heating intensity.
Be that the sheet material forming shape that to be automobile cover plate or wheel make regulation with the parts of sheet material etc. is used.For the desired characteristic of the aluminium plate that uses on this base part be: comprehensively have when being shaped high formability that shape in accordance with regulations is shaped and the parts high strength when using, reliability is met.
As the material with such overall characteristic, generally using Al-Mg is that alloy and Al-Mg-Si are the sheet material of alloy.The feature of Al-Mg alloy is to have medium intensity, and plasticity is good especially, and Al-Mg-Si is that the feature of alloy then is that plasticity is poorer slightly than Al-Mg alloy, but increases through the japanning heating intensity.So complex-shaped parts tend to use the Al-Mg alloy, requiring high-intensity parts then often to use Al-Mg-Si is alloy.
In the past, the Al-Mg-Si that provides for this purpose is the manufacture method of alloy, the ingot casting that normally will adopt die casting (DC) to make earlier is heated to 400-550 ℃ and implements the homogenizing processing, cool to room temperature or begin hot rolling then without cooling off in 400-500 ℃ temperature range, and in 350-400 ℃ temperature range, finish hot rolling.
For removing the heterogeneous structure layer on ingot casting top layer, before homogenizing is handled or afterwards, usually carry out plane turning.The hot rolled sheet material that is through with like this carries out cold rollingly subsequently, carries out as required in cold-rolled process or does not carry out process annealing, and precision work reaches predetermined thickness of slab.
The sheet material of cold rolling end of a period heats several seconds-a few hours at 480-580 ℃, carries out solution treatment, carries out chilling by modes such as water-cooled or forced air-coolings then and quenches.After this, as required, to gently process in order to align also sometimes.
Natural aging at room temperature takes place in the sheet material after the chilling solid solution, causes that intensity increases, but wants just can make 1-4 day stable performance to get off.When common room temperature was placed, the natural aging under the room temperature reduced japanning roasting hardening thereafter, and this point is known, and people also know in addition, and natural aging is carried out after quenching immediately, and natural aging is the most remarkable between a few days after quenching.
Therefore, improve this purpose, propose or implemented: 1. after solution treatment for reaching the heat hardening that makes when japanning etc., implement a few hours 50-150 ℃ low-temperature heat immediately, or 2. after the solution treatment, at room temperature place, carry out a few hours 50-300 ℃ heating then, or the like.
1. processing, be will be before carrying out natural aging, generate by heating and to give roasting indurative precipitated phase, to improve the roasting hardening, on the other hand, 2. processing is implemented as stabilization treatment, its objective is after the solution treatment and after the rapid natural aging of a few days roughly is over, and the mechanical property that the result that the natural aging of placing because of long-time room temperature is slowly carried out causes changes and is limited in minimum degree.
In recent years, the fuel cost of automobile improves constantly, and the operability of people's strong request electric product and mechanical part, efficient improve in addition, and is therefore very strong to the light-weighted requirement of these article components.Be subjected under the situation about requiring like this, the wall thickness of parts constantly reduces, and requires as the aluminium of raw material high strength more.
Therefore be that the higher level research of heat hardening of alloy is carried out with might and main to Al-Mg-Si.But Al-Mg is an alloy relatively, and Al-Mg-Si is that the plasticity of alloy is relatively poor, has therefore hindered the use that the Al-Mg-Si that demonstrates high heat hardening is an alloy.For this reason, about plasticity also seeking with its improve become with Al-Mg be the equal above level of alloy.
Meanwhile, viewpoint from the raising of enamelling process efficient, heating condition trends towards low temperature and short period of timeization, this has constituted the condition that is adopted again, and to be difficult to make Al-Mg-Si be alloy hardened tendency, under such background, higher heat hardening and the good sheet material of the good isostatic of plasticity are developed in strong hope.
As previously mentioned, the conduct in past improves the method for heat hardening, be known that after solution treatment in the 80-150 ℃ of heating of carrying out 1 hour-a few hours, and know that its effect can obtain higher effect than the situation of carrying out heat treated before natural aging takes place.
But, before taking place, heat-treat in natural aging behind solid solution, the chilling, must heat in the short period of time, therefore in case implement as industrial mode, then can not obtain stable properties, in same manufactured materials, produce deviation because be subjected to room temperature after the solution treatment, before the thermal treatment and the influence of room temperature storage period greatly.And conclude plasticity deterioration when implementing this processing.In addition, when carrying out heat treated after natural aging, the reduction of plasticity is little, and it also is possible by the change condition plasticity being improved, but the raising effect of heat hardening is little.
The inventor is that tissue the sheet alloy is started with from Al-Mg-Si, carry out detailed research, the result has finished the present invention, in more detail, by the heat treated after hot rolling and the solution treatment is combined, obtain having the high plasticity and the tissue of heat hardening.
That is to say, the present invention is the manufacture method of the good aluminum alloy plate materials of a kind of plasticity and heat hardening, it is characterized in that, making by containing necessary composition Mg0.2-1.5% (weight), Si0.4-2.0% (weight), and contain below the Cu1.5% (weight), below the Zn2.0% (weight), below the Cr0.5% (weight), below the Mn1.0% (weight), below the Zr0.3% (weight), below the Ti0.1% (weight), any or two or more during V0.2% (weight) is following, when surplus is the common aluminum alloy plate materials that impurity and Al formed, ingot casting or milled sheet are heated to more than 480 ℃, when carrying out hot rolling, in 360 ℃-450 ℃ temperature range, do not stop more than 15 minutes, the finishing temperature scope is below 360 ℃, carry out cold rolling then, add process annealing in case of necessity, roll into after the predetermined thickness of slab, carry out solution treatment more than 10 seconds in the heating of the temperature more than 450 ℃, then at room temperature implement the natural aging more than 1 hour, make conductivity of electrolyte materials become the scope of 35-55%IACS, then in 180-300 ℃ temperature range, carry out more than 10 seconds with the scope that does not reduce specific conductivity in fact, 10 minutes with interior heat treated, and with the average crystal grain diameter that plate face before and after this heat treated parallels in the face is below the 90 μ m, and the length of the crystal grain diameter of rolling direction and perpendicular direction than (rolling direction length/vertical-direction length) on average between 0.5-4, the average maximum length that contains the Si compound in the material is below the 10 μ m.
Below narration limits the reason of forming as the aluminium alloy of object of the present invention.
Mg and Si are the main adding elements as the alloy of object of the present invention, and they are the state of solid solution condition and the fine precipitate of generation after solutionizing, thermal treatment, give material with plasticity, when the shaping post-heating, make the fine precipitate growth that exists before the heating, give heat hardening.
Heat hardening step-down when Mg less than 0.2% (weight), Si less than 0.4% (weight), in addition, the Mg addition surpasses 1.5% (weight), plasticity worsened when the Si addition surpassed 2.0% (weight).
Cu and Zn have the effect that improves plasticity, but the tendency of some reduction erosion resistances is arranged, and can determine as required to add or do not add.When Cu surpassed 1.5% (weight), Zn above 2.0% (weight), plasticity reduced.
Cr, Mn, Zr, Ti, V have the effect that makes material structure refinement, homogenizing, but the Cr addition surpasses 0.5% (weight), the Mn addition surpasses 0.3% (weight), Ti addition above 0.1% (weight), when the V addition surpasses 0.2% (weight) above 1.0% (weight), Zn addition, generate thick compound in the material, the plasticity of material is reduced.
Except that above-mentioned, the major impurity in the alloy is Fe, and iron-holder does not hinder effect of the present invention when 0.5% (weight) is following.Other impurity, trace element need only below 0.1% (weight) with regard to not overslaugh effect of the present invention.
The reason of following descriptive provision manufacturing process of the present invention.
Casting of the present invention can be according to usual method.
One of principal character of manufacture method of the present invention is its hot-rolled condition.By controlling this hot-rolled condition, make the organizational controls after the solution treatment in the subsequent handling become possibility, and heat treated effect increase.
Manufacture method of the present invention for the Al-Mg-Si that improves as object is each characteristic of alloy, must make Mg, Si solid solution as much as possible when solution treatment.At the means that reach this purpose, the contriver is alloy organizing behavior research repeatedly at length with regard to Al-Mg-Si.Manufacture method of the present invention is exactly the result of this research.
That is to say,, must improve the Mg before the solution treatment, the solid solubility of Si as far as possible for making Mg, Si solid solution capacity become maximum when the solution treatment, simultaneously, also must make contain these elements, particularly to contain the compound size of Si tiny and disperse.
These compounds carry out solid solution reaction by material is at high temperature heated, and the compound volume ratio in the material reduces, and solid solubility increases.Therefore, material is as far as possible at high temperature heated, for reducing above-mentioned volume ratio, the increase solid solution capacity that contains the Si compound, it is highly effective improving heat hardening.
But only heat can't make these compound completely dissolves.Though the overall volume ratio of compound reduces, each remaining after heat compound size is also bigger than the compound size before heating.
In addition, when pressing method hot rolling in the past, heated material temperature in the operation of rolling descends, and at the end rolling in rolling neutralization, above-mentioned Mg, Si compound are separated out once more.
This feature of separating out again is, above-mentioned remaining thickization of compound and take place in hot rolling or the recrystal grain border that generates after the rolling end of a period is preferentially separated out and grown.And, this evolution reaction is owing to be bigger than reaction under the comparatively high temps thereby speed of separating out, distortion when adding hot rolling also promotes this separating out, therefore just be grown to serve as thick precipitated phase at short notice, thick precipitated phase like this is difficult to solid solution when solution treatment, this fact is identified.
Therefore, separating out again when suppressing this hot rolling, take and to be heated to pyritous material rolling at low temperatures method after the cooling rapidly in the middle of the homogenizing processing etc., find to do like this and have the effect that reduces speed of separating out, while is the refinement recrystal grain effectively, makes towards the situation of preferentially separating out and growing of crystal boundary to obtain disperseing.
The present invention finishes based on such technological thought, below the reason that regulation is created conditions among narration the present invention.
Heating temperature before rolling must be decided to be high temperature, so that contain the solid solution as much as possible of Si compound.Then solid solution is insufficient in the heating that the employing less than is 450 ℃.Preferred Heating temperature is more than 480 ℃.The upper limit of Heating temperature is not made special regulation.Temperature is higher best, as long as be no more than the solidus temperature of material.
During hot rolling, in 360-450 ℃ temperature range, carry out rolling make to separate out the most easily carry out, and this also is to make the big condition of the easy chap of recrystal grain.Thereby must cool off at short notice by this temperature range.If in this temperature range, stop more than 15 minutes, then generate above-mentioned thick precipitate, make greatly deterioration of plasticity, heat hardening all deteriorations, particularly heating property.Therefore be advisable with interior at 10 minutes.
But under the bigger situation of the wall thickness of ingot casting, quick cooling is difficult, so the method that adopts as hope is through being thought of as:
1. use little ingot casting of wall thickness or milled sheet, so that the cooling in rolling is carried out rapidly.
Take heavy reduction when 2. rolling, thickness of slab is reduced rapidly, be rolled at short notice refrigerative wall thickness easily.
3. in rolling way, energetically water, wet goods heat-eliminating medium are added in the milled sheet, realize quick cooling whereby.
The present invention does not make specified in more detail to these conditions, as long as can satisfy said temperature, time conditions.
Hot rolling finishing temperature is defined as below 360 ℃, when hot rolling finishing temperature surpasses 360 ℃, and thickization of recrystal grain, plasticity, heat hardening be deterioration all.
The sheet material that hot rolling ends carries out cold rolling again, carries out in cold rolling way as required or does not carry out process annealing, rolls into predetermined thickness of slab, heats more than 10 seconds in the temperature more than 450 ℃ then, carries out solution treatment.
It is insufficient that temperature that less than is 450 ℃ or 10 seconds heating of less than are carried out solid solution, therefore heat hardening, plasticity all reduced.The upper limit to Heating temperature is not done special stipulation, and normally the temperature below solidus temperature is implemented.In addition, heat-up time is long more, and is favourable more to the carrying out of solid solution, becomes unfavorable economically but cross long heating, therefore determines that by operational situation be good heat-up time.
Be decided to be more than 1 hour to next thermal treatment natural aging time before after the solution treatment.Natural aging time in short-term, material property instability after heat treatment has the danger that makes the plasticity deterioration because of the material that can not get homogeneous thereafter.The upper limit to natural aging time is not done special stipulation, though after the solution treatment through also can obtaining same effect more than 1 year, but industrially normally in 1 month, implement.In addition, the electric conductivity of material is decided to be 35-55%IACS after the natural aging.No matter be to surpass the upper limit of this scope or be lower than its lower limit, heat hardening all reduces.
Two of principal character of the present invention is the heat treated after the solution treatment.
The purpose of heat treated of the present invention is, around GP zone that generates when making natural aging after the solid solution and crystal boundary periphery and the thick intermetallic compound, particularly also solid solution is spread in the enrichment of the Mg that generates around the intermetallic compound that contains Si, Si solute mutually.Thereby above-mentioned each characteristic is effectively improved become possibility.
Specifically, with after the solution treatment at room temperature the material of embodiment natural aging more than 1 hour in 180-300 ℃ temperature range, carry out more than 10 seconds, in 10 minutes, be preferably more than 1 minute, 10 minutes with interior heat treated.180 ℃ of Heating temperature less thaies or heat-up time less than in the time of 10 seconds, can improve plasticity well and heat hardening causes difficulty to equilibrium.In addition, Heating temperature surpasses 300 ℃ or when surpassing 10 minutes heat-up time, plasticity and heat hardening reduction.
In addition, this diffusion heat treatments must be carried out in the scope that specific conductivity does not reduce.Specific conductivity is to embody the solid solution capacity in the material and the index of the amount of separating out, and when specific conductivity reduced, the effect of diffusion heat treated can not be given full play to, and makes plasticity, heat hardening reduction.Therefore would rather wish that specific conductivity increases.
In addition,, consider the standard deviation of mensuration, should take ± 0.5%IACS as limit of error, if in this scope, reduce then can be judged as the variation that specific conductivity does not have essence about the mensuration of specific conductivity.As for the relation of heat treated condition and specific conductivity, owing to influenced by alloying constituent, the heat treated condition that does not therefore reduce specific conductivity should decide according to the composition of alloy.
In addition, average crystal grain diameter in the face that the plate face forward and backward with spreading heat treated parallels is below the 90 μ m, and on average between 0.5-4, the average maximum length of siliceous compound is to be necessary below the 10 μ m to the length of the crystal grain diameter of rolling direction and vertical direction thereof in the material than (rolling direction length/vertical-direction length).
Above said " with the average crystal grain diameter in the face that the plate face parallels ", " the average maximum length of compound ", be not along specific directions such as rolling direction, its vertical direction, but mean the size on all directions.
Parallel the length of crystal grain diameter that average crystal grain diameter in the face surpasses 90 μ m or rolling direction and its vertical direction with diffusion heat treated front face than (rolling direction length/vertical-direction length) average average maximum length that contains the Si compound outside the 0.5-4 scope or in the material during above 10 μ m, the effect of diffusion heat treated reduces, and heat hardening, plasticity also all reduce.
In addition, parallel average crystal grain diameter in the face with the plate face of diffusion after the heat treated when surpassing 90 μ m, can produce the macroscopic irregularity that is called orange peel during shaping.Rolling direction and the length of the crystal grain diameter of its vertical direction of diffusion after the heat treated is average beyond the 0.5-4 scope or the average maximum length that contains the Si compound in the material when surpassing 10 μ m than (rolling direction length/vertical-direction length), the plasticity reduction.
Preferably, with the average crystal grain diameter in the face that diffusion heat treatments front and rear panel face parallels is below the 80 μ m, the length of the grain size of the perpendicular direction of rolling direction is than the scope of (rolling direction length/vertical-direction length) average out to 0.6-3, and the average maximum length that contains the Si compound in the material is below the 8 μ m.
Make the raising of each characteristic by this diffusion heat treated, combined with aforesaid hot-rolled condition, can bring into play its effect to greatest extent, even only also produce effect with the diffusion heat treated, but that its effect is wanted is littler.In addition, as long as this diffusion heat treated satisfies heating condition, then can with the heat treated double as of oiling, drying, surface treatment etc., this is self-evident.
Embodiment
One embodiment of the present of invention below are described.
Alloy with composition shown in the common DC castmethod casting table 1 obtains thickness 400mm, and the ingot casting of wide 120mm carries out hot rolling with this ingot casting by the condition of table 2, rolls into the sheet material of thick 7mm.The sheet material of the thick 1.0mm of cold rolling again one-tenth.After this sheet material being pressed the condition solution treatment of table 2, in being chilled to room temperature, under room temperature, place, and then implement the diffusion heat treated of table 2, as on approbation sheet material by the specified time shown in the table 2 by forced air-cooling.
Measure the average maximum length of compound on the diffusion heat treated front and rear panel surface of each material after to surface finish with scanning electronic microscope, the mean value of the aspect ratio (rolling direction length/vertical-direction length) of plate surface average crystal grain diameter and relative its rolling direction then is with the etch of triumphant Le Shi liquid after surface finish, use light microscope determining, specific conductivity δ test determination.The results are shown in table 3.Estimate plasticity, heat hardening with following test conditions in addition.
(1) formability test: test as deep drawability, behind the lubricating oil of coating 5CSt on the specimen surface that cuts into φ 84mm, use the cylinder drift of diameter 40mm, shoulder R3mm, test with the condition of drift speed 120mm/min, wrinkle resistant pressure 3000kgf.Test-results adopts shapable maximum height to estimate.
In addition, as the bulging test,, estimate its plasticity with the maximum height that does not crack with the method that the Erichsen test A of JIS Z2247 specification is pressed in No. 2 sample enforcement.Observe the surface after being shaped in addition, estimate whether produce orange peel.
(2) heat hardening test
Goods shaping raw material endurance is the smaller the better before the baking vanish application, but shows that in as the various molded components of goods the endurance value behind its anti-deformed finger target baking vanish is then high more good more.Thereby carry out 175 ℃ * 60 minutes heating as the simulation of japanning heating, by because the endurance that heating produces increases share judgement heat hardening.
These be the results are shown in table 4.
Table 1
| Alloy No | ???Mg | ???Si | ??Cu | ??Zn | ???Cr | ???Mn | ???Zr | ???Ti | ??V | ????Al | |
| Example of the present invention | ???1 | ??0.5 | ??1.0 | ??— | ??— | ??0.03 | ???— | ??0.03 | ??0.01 | ??— | Surplus |
| ???2 | ??1.0 | ??1.0 | ?0.8 | ??— | ???— | ??0.12 | ??0.04 | ??0.01 | ?0.05 | ????″ | |
| ???3 | ??0.8 | ??1.3 | ??— | ?0.2 | ???— | ??0.06 | ???— | ??0.04 | ??— | ????″ | |
| Comparative example | ???4 | ??0.02 | ??0.03 | ?0.5 | ??— | ??0.03 | ???— | ???— | ??0.02 | ??— | ????″ |
| ???5 | ??1.8 | ??2.6 | ??— | ?0.5 | ???— | ???— | ???— | ??0.01 | ??— | ????″ | |
| ??5182 | ??4.5 | ??0.08 | ??— | ??— | ???— | ??0.25 | ???— | ??0.02 | ??— | ????″ |
(notes) composition is wt%
Table 2
| Operation number | The hot rolling Heating temperature | 360～450 ℃ time | Finishing temperature | Solution treatment | Natural aging time | The diffusion heat treated | |
| Example of the present invention | ?A | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 5 hours | 190 ℃ * 9 minutes |
| ?B | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 2 hours | 200 ℃ * 5 minutes | |
| ?C | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 10 days | 250 ℃ * 2 minutes | |
| ?D | ???550℃ | 7 minutes | ?290℃ | 500 ℃ * 10 seconds | 26 days | 270 ℃ * 15 seconds | |
| Comparative example | ?E | ???440℃ | 45 minutes | ?280℃ | 540 ℃ * 30 seconds | 8 hours | 250 ℃ * 2 minutes |
| ?F | ???520℃ | 25 minutes | ?320℃ | 540 ℃ * 30 seconds | 3 days | 250 ℃ * 2 minutes | |
| ?G | ???550℃ | 10 minutes | ?420℃ | 550 ℃ * 60 seconds | 8 hours | 250 ℃ * 2 minutes | |
| ?H | ???520℃ | 5 minutes | ?280℃ | 400 ℃ * 10 minutes | 1 day | 250 ℃ * 2 minutes | |
| ?I | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 25 minutes | 290 ℃ * 2 minutes | |
| ?J | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | ????— | Not heating | |
| ?K | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 6 hours | 100 ℃ * 10 minutes | |
| ?L | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 4 days | 280 ℃ * 30 minutes | |
| ?M | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 12 hours | 350 ℃ * 3 minutes | |
| ?N | ???520℃ | 5 minutes | ?280℃ | 540 ℃ * 30 seconds | 8 hours | 190 ℃ * 5 seconds |
Table 3
| Test piece number (Test pc No.) | Alloy number | Operation number | Before the diffusion heating | After the diffusion heating | ||||||||
| Average crystal grain size μ m | Aspect ratio is average | Compound on average greatly enhances most μ m | Specific conductivity % IACS | Average crystal grain size μ m | Aspect ratio is average | Compound on average greatly enhances most μ m | Specific conductivity % IACS | Conductivity variations % IACS | ||||
| Example of the present invention | ?(1) | ????1 | ??A | ???36 | ???2.1 | ???3.6 | ???44.1 | ???36 | ???2.0 | ????3.6 | ??45.0 | ???+0.9 |
| ?(2) | ????1 | ??B | ???35 | ???2.0 | ???3.4 | ???44.0 | ???34 | ???2.1 | ????3.5 | ??45.2 | ???+1.2 | |
| ?(3) | ????1 | ??C | ???35 | ???1.9 | ???3.6 | ???44.4 | ???35 | ???1.9 | ????3.4 | ??45.7 | ???+1.3 | |
| ?(4) | ????1 | ??D | ???31 | ???2.5 | ???4.8 | ???45.3 | ???30 | ???2.3 | ????4.6 | ??46.1 | ???+0.8 | |
| ?(5) | ????2 | ??B | ???28 | ???1.2 | ???4.2 | ???41.2 | ???29 | ???1.3 | ????4.1 | ??42.4 | ???+1.2 | |
| ?(6) | ????3 | ??B | ???51 | ???1.0 | ???5.1 | ???40.2 | ???52 | ???0.9 | ????5.0 | ??41.1 | ???+0.9 | |
| Comparative example | ?(7) | ????1 | ??E | ???32 | ???2.2 | ??15.2 | ???47.2 | ???34 | ???2.1 | ???15.1 | ??47.7 | ???+0.5 |
| ?(8) | ????1 | ??F | ???37 | ???1.9 | ??11.2 | ???46.1 | ???37 | ???1.8 | ???11.1 | ??46.7 | ???+0.6 | |
| ?(9) | ????1 | ??G | ???95 | ???1.0 | ??10.4 | ???45.8 | ???05 | ???1.1 | ???10.4 | ??46.6 | ???+0.8 | |
| ?(10) | ????1 | ??H | ???45 | ???5.2 | ??12.1 | ???50.1 | ???27 | ???5.1 | ???12.5 | ??50.5 | ???+0.4 | |
| ?(11) | ????1 | ??I | ???37 | ???2.1 | ???3.2 | ???44.2 | ???36 | ???2.4 | ????3.5 | ??43.4 | ???-0.8 | |
| ?(12) | ????1 | ??J | ???36 | ???1.9 | ???3.0 | ???44.1 | ???— | ????— | ????— | ???— | ????— | |
| ?(13) | ????1 | ??K | ???37 | ???2.0 | ???3.1 | ???44.7 | ???38 | ???2.2 | ????2.9 | ??44.1 | ???-0.6 | |
| ?(14) | ????1 | ??L | ???36 | ???2.0 | ???2.9 | ???44.0 | ???40 | ???1.8 | ????3.2 | ??42.3 | ???-1.1 | |
| ?(15) | ????1 | ??M | ???35 | ???2.2 | ???3.0 | ???44.1 | ???42 | ???1.7 | ????3.4 | ??42.8 | ???-1.3 | |
| ?(16) | ????1 | ??N | ???34 | ???1.9 | ???2.8 | ???43.9 | ???34 | ???2.0 | ????3.0 | ??42.8 | ???-1.1 | |
| ?(17) | ????4 | ??B | ??108 | ???0.8 | ???1.0 | ???56.2 | ??1.9 | ???0.9 | ????0.9 | ??56.1 | ???-0.1 | |
| ?(18) | ????5 | ??B | ???37 | ???1.2 | ??16.2 | ???40.1 | ???37 | ???1.1 | ???16.4 | ??41.1 | ???+1.0 | |
| ?(19) | ??5182 | ??B | ???40 | ???1.3 | ???2.8 | ???31.3 | ???41 | ???1.2 | ????3.2 | ??31.5 | ???+0.2 | |
Table 4
| Test piece number (Test pc No.) | Alloy number | Operation number | Plasticity | Heat hardening | |||||
| Deep drawing quality | Bulging | Orange peel | Endurance before the heating | Heating back endurance | Endurance increases | ||||
| Example of the present invention | ?(1) | ???1 | ??A | ????8.9mm | ??0.6mm | Do not have | ???142MPa | ???267MPa | ???125MPa |
| ?(2) | ???1 | ??B | ????9.7mm | ??9.7mm | Do not have | ???151MPa | ???281MPa | ???130MPa | |
| ?(3) | ???1 | ??C | ????9.8mm | ??9.9mm | Do not have | ???149MPa | ???272MPa | ???123MPa | |
| ?(4) | ???1 | ??D | ????9.7mm | ??9.8mm | Do not have | ???125MPa | ???251MPa | ???126MPa | |
| ?(5) | ???2 | ??B | ????10.0mm | ??9.8mm | Do not have | ???161MPa | ???269MPa | ???108MPa | |
| ?(6) | ???3 | ??B | ????9.7mm | ??9.7mm | Do not have | ???162MPa | ???271MPa | ???109MPa | |
| Comparative example | ?(7) | ???1 | ??E | ????8.9mm | ??9.1mm | Do not have | ???144MPa | ???222MPa | ????78MPa |
| ?(8) | ???1 | ??F | ????9.1mm | ??9.4mm | Do not have | ???151MPa | ???236MPa | ????85MPa | |
| ?(9) | ???1 | ??G | ????9.0mm | ??9.1mm | Have | ???148MPa | ???219MPa | ????71MPa | |
| ?(10) | ???1 | ??H | ????8.8mm | ??8.9mm | Do not have | ???129MPa | ???161MPa | ????32MPa | |
| ?(11) | ???1 | ??I | ????8.2mm | ??8.7mm | Do not have | ???151MPa | ???270MPa | ???119MPa | |
| ?(12) | ???1 | ??J | ????9.0mm | ??9.4mm | Do not have | ???153MPa | ???218MPa | ????65MPa | |
| ?(13) | ???1 | ??K | ????9.0mm | ??9.3mm | Do not have | ???181MPa | ???212MPa | ????31MPa | |
| ?(14) | ???1 | ??L | ????8.0mm | ??7.8mm | Do not have | ???153MPa | ???232MPa | ????79MPa | |
| ?(15) | ???1 | ??M | ????8.2mm | ??8.7mm | Do not have | ???187MPa | ???221MPa | ????33MPa | |
| ?(16) | ???1 | ??N | ????8.9mm | ??9.2mm | Do not have | ???146MPa | ???212MPa | ????66MPa | |
| ?(17) | ???4 | ??B | ????9.7mm | ??10.2mm | Have | ????59MPa | ????61MPa | ?????2MPa | |
| ?(18) | ???5 | ??B | ????8.7mm | ??8.1mm | Do not have | ???172MPa | ???250MPa | ????87MPa | |
| ?(19) | ??5182 | ??B | ????11.7mm | ??10.0mm | Do not have | ???132MPa | ???127MPa | ????-5MPa | |
As indicated by table 1-table 4, sample No. (1)-(6) are embodiments of the invention, and its plasticity, heat hardening are all good as can be known.
Sample No. (7)-(9) are the comparative example of hot-rolled condition outside the scope of the invention, and its plasticity, heat hardening are simultaneously all poor as can be known.
Sample No. (10) is the comparative example of solid solution condition outside the scope of the invention, its plasticity, heat hardening inequality as can be known, and heat hardening is poor especially.
Sample No. (11) is the comparative example of natural aging condition outside the scope of the invention after the solution treatment, can find out that its plasticity is poor.
Sample No. (12) is a comparative example of not implementing diffusion heat treatments after the solution treatment, and its heat hardening is poor as can be known.
Sample (13)-(16) are the comparative example of diffusion heat treatments condition outside the scope of the invention after the solution treatment, can find out plasticity, heat hardening inequality simultaneously.
Sample (17)-(18) are the comparative example of alloying constituent outside the scope of the invention, and the heat hardening of (17) is poor as can be known, and the plasticity of (18), heat hardening be inequality simultaneously.
Sample No. (19) is existing material JIS5182 alloy, and its plasticity and material of the present invention are equal or more excellent as can be known, but the non-constant of thermosetting.
As discussed above, it is all good to adopt the present invention can produce plasticity, heat hardening, after processing such as the shaping of body of a motor car, electric component etc., carry out the suitable light sheet of the slab products that uses behind the baking vanish, therefore reached industrial unusual effect.
Claims (1)
1. the manufacture method of the good aluminum alloy plate materials of plasticity and heat hardening, it is characterized in that, making by containing necessary composition Mg0.2-1.5% (weight), Si0.4-2.0% (weight), contain in addition below the Cu1.5% (weight), below the Zn2.0% (weight), below the Cr0.5% (weight), below the Mn1.0% (weight), below the Zr0.3% (weight), below the Ti0.1% (weight), more than any one or two kinds of during V0.2% (weight) is following, when surplus is the aluminum alloy plate materials that common impurity and Al formed, ingot casting or milled sheet are heated to more than 480 ℃, when carrying out hot rolling, in 360-450 ℃ temperature range, do not stop more than 15 minutes, the finishing temperature scope is below 360 ℃, carry out cold rolling then, and add process annealing as required, roll into predetermined thickness of slab, then, carry out solution treatment more than 10 seconds in the heating of the temperature more than 450 ℃, then at room temperature carry out the natural aging more than 1 hour, make conductivity of electrolyte materials become the scope of 35-55%IACS, then in 180-300 ℃ temperature range, carry out more than 10 seconds with the scope that does not reduce specific conductivity in fact, 10 minutes with interior heat treated, and with the average crystal grain diameter in the face that parallels of plate face before and after the thermal treatment is below the 90 μ m, and on average between 0.5-4, the average maximum length that contains the Si compound in the material is below the 10 μ m to the length of the crystal grain diameter of the perpendicular direction of rolling direction than (rolling direction length/vertical-direction length).
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP135797/94 | 1994-06-17 | ||
| JP6135797A JPH083702A (en) | 1994-06-17 | 1994-06-17 | Production of aluminum alloy sheet material excellent in formability and heating hardenability |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN1141958A true CN1141958A (en) | 1997-02-05 |
Family
ID=15160054
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN95107003A Pending CN1141958A (en) | 1994-06-17 | 1995-06-15 | Method for production of aluminium alloy plate with good characteristics of shaping and thermo hardening |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JPH083702A (en) |
| KR (1) | KR960001157A (en) |
| CN (1) | CN1141958A (en) |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN100360249C (en) * | 2006-06-30 | 2008-01-09 | 郑州铝业股份有限公司 | Short process production technology of ultrathin aluminium foil |
| CN100378237C (en) * | 2006-04-25 | 2008-04-02 | 东北轻合金有限责任公司 | Method of preparing aviation alloyed aluminium variable section sheets |
| CN100419116C (en) * | 2006-03-14 | 2008-09-17 | 东北大学 | Preheat treatment for improving automobile plate of 6111 aluminium alloy formation and baking paint hardening performance |
| CN100491579C (en) * | 2003-03-17 | 2009-05-27 | 克里斯铝轧制品有限公司 | Method for producing an integrated monolithic aluminium structure and aluminium product machined from that structure |
| CN103429772A (en) * | 2011-03-15 | 2013-12-04 | 株式会社神户制钢所 | Aluminum alloy plate having superior baking finish hardening |
| CN105026588A (en) * | 2013-03-07 | 2015-11-04 | 阿莱利斯铝业迪弗尔私人有限公司 | Sintered body, and sputtering target for magnetic recording film formation use which comprises said sintered body |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3729605B2 (en) * | 1997-06-19 | 2005-12-21 | 株式会社神戸製鋼所 | Method for producing aluminum alloy sheet with excellent bake hardenability and reduced aging at room temperature |
| JP4274674B2 (en) * | 2000-04-12 | 2009-06-10 | トヨタ自動車株式会社 | Aluminum alloy member excellent in crushability and manufacturing method thereof |
-
1994
- 1994-06-17 JP JP6135797A patent/JPH083702A/en active Pending
-
1995
- 1995-06-15 CN CN95107003A patent/CN1141958A/en active Pending
- 1995-06-17 KR KR1019950016563A patent/KR960001157A/en not_active Application Discontinuation
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN100491579C (en) * | 2003-03-17 | 2009-05-27 | 克里斯铝轧制品有限公司 | Method for producing an integrated monolithic aluminium structure and aluminium product machined from that structure |
| CN100419116C (en) * | 2006-03-14 | 2008-09-17 | 东北大学 | Preheat treatment for improving automobile plate of 6111 aluminium alloy formation and baking paint hardening performance |
| CN100378237C (en) * | 2006-04-25 | 2008-04-02 | 东北轻合金有限责任公司 | Method of preparing aviation alloyed aluminium variable section sheets |
| CN100360249C (en) * | 2006-06-30 | 2008-01-09 | 郑州铝业股份有限公司 | Short process production technology of ultrathin aluminium foil |
| CN103429772A (en) * | 2011-03-15 | 2013-12-04 | 株式会社神户制钢所 | Aluminum alloy plate having superior baking finish hardening |
| CN103429772B (en) * | 2011-03-15 | 2015-08-26 | 株式会社神户制钢所 | The aluminium alloy plate of bake hardening excellence |
| CN105026588A (en) * | 2013-03-07 | 2015-11-04 | 阿莱利斯铝业迪弗尔私人有限公司 | Sintered body, and sputtering target for magnetic recording film formation use which comprises said sintered body |
| CN105026588B (en) * | 2013-03-07 | 2017-08-25 | 阿莱利斯铝业迪弗尔私人有限公司 | The manufacture method of Al Mg Si alloy rolled sheet products with excellent mouldability |
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| CN110475885B (en) * | 2017-03-29 | 2021-08-24 | 古河电气工业株式会社 | Aluminum alloy material, and conductive member, battery member, fastening member, spring member, and structural member using same |
| CN113166858A (en) * | 2018-12-11 | 2021-07-23 | 新布里萨什肯联铝业 | Method for producing 6XXX aluminium sheets with high surface quality |
| CN113166858B (en) * | 2018-12-11 | 2023-03-03 | 新布里萨什肯联铝业 | Method for producing 6XXX aluminium sheets with high surface quality |
| CN110714147A (en) * | 2019-11-05 | 2020-01-21 | 郑州明泰实业有限公司 | 6082 aluminum alloy plate for aviation and production process thereof |
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Also Published As
| Publication number | Publication date |
|---|---|
| JPH083702A (en) | 1996-01-09 |
| KR960001157A (en) | 1996-01-25 |
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