CN103459629B - Heat exchanger aluminum alloy fin material and manufacture method thereof for attenuate stretching and punching - Google Patents

Heat exchanger aluminum alloy fin material and manufacture method thereof for attenuate stretching and punching Download PDF

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Publication number
CN103459629B
CN103459629B CN201280015567.5A CN201280015567A CN103459629B CN 103459629 B CN103459629 B CN 103459629B CN 201280015567 A CN201280015567 A CN 201280015567A CN 103459629 B CN103459629 B CN 103459629B
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fin material
heat exchanger
punching
aluminum alloy
quality
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CN103459629A (en
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金田大辅
梅田秀俊
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Kobe Steel Ltd
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Kobe Steel Ltd
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Priority claimed from JP2011080855A external-priority patent/JP5828657B2/en
Priority claimed from JP2011080853A external-priority patent/JP5843462B2/en
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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C21/00—Alloys based on aluminium
    • 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
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F21/00—Constructions of heat-exchange apparatus characterised by the selection of particular materials
    • F28F21/08—Constructions of heat-exchange apparatus characterised by the selection of particular materials of metal
    • F28F21/081—Heat exchange elements made from metals or metal alloys
    • F28F21/084—Heat exchange elements made from metals or metal alloys from aluminium or aluminium alloys
    • F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
    • F28—HEAT EXCHANGE IN GENERAL
    • F28F—DETAILS OF HEAT-EXCHANGE AND HEAT-TRANSFER APPARATUS, OF GENERAL APPLICATION
    • F28F2215/00—Fins

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Organic Chemistry (AREA)
  • Thermal Sciences (AREA)
  • Physics & Mathematics (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • General Engineering & Computer Science (AREA)
  • Metal Rolling (AREA)
  • Shaping Metal By Deep-Drawing, Or The Like (AREA)
  • Laminated Bodies (AREA)

Abstract

The invention provides a kind of attenuate stretching and punching heat exchanger aluminum alloy fin material, it is characterized in that, the resistance to collar disruptiveness excellence of heat exchanger aluminum alloy fin material for this attenuate stretching and punching, the fin material of using taking attenuate stretching and punching is object, can be suppressed at is shaped adds the generation that the collar in man-hour breaks, described attenuate stretching and punching with heat exchanger aluminum alloy fin material by containing Fe:0.010～0.4 quality %, remainder comprises Al and inevitable impurity, Al purity is that aluminium alloys more than 99.30 quality % forms, described attenuate stretching and punching is less than 0.115mm with the thickness of heat exchanger aluminum alloy fin material, the average grain diameter of subgrain is below 2.5 μ m and yield strength is 130N/mm2Above. Be further characterized in that the intermetallic compound that maximum length exceedes 3 μ m is 2000/mm2Below.

Description

Heat exchanger aluminum alloy fin material and manufacture method thereof for attenuate stretching and punching
Technical field
The attenuate stretching and punching (drawlesspress) that the present invention relates to use in heat exchanger is used heat exchangeAluminum alloy fin material and manufacture method thereof for device.
Background technology
In recent years, aluminum alloy fin material for the heat exchanger using in the heat exchangers such as air-conditioner (it is following,Suitably be called fin material) in, according to the replacement to new refrigerant, air-conditioning along with freon restrictionMiniaturization, lightweight or the high performance etc. of device self, day by day realize thin-walled property and thickness of slab existedBelow 0.15mm, realize thin-walled property recently until 0.09mm left and right.
At this, the forming process of fin material has stretching mode, attenuate stretching mode and stretching attenuate and drawsStretch complex method (collocation mode). Stretching mode comprises overhanging operation, coil buckling operation, perforation (thornWear) and reaming operation (plunging), outer Zhang Gong's order, attenuate stretching mode comprises perforation and reamingOperation, smooth out with the fingers and drag (thinning) operation, outer Zhang Gong's order, collocation mode mainly comprises overhanging operation, coil bucklingOperation, perforation and reaming operation, attenuate stretching process, outer Zhang Gong's order.
In above-mentioned forming process arbitrarily, for the thorn of the effective hole collar (collar) of the copper pipe that is shapedWear with plunging and be shaped and outer the forming process that is absolutely necessary for fin material that is shaped. ButBe, above-mentioned shaping for realizing thin-walled property until thickness of slab is to become the fin material below 0.15mmToo harsh shaping. Therefore, corresponding with above-mentioned thin-walled property, exploitation has been improved the wing of processabilitySheet material.
For example, in patent documentation 1, disclose the aluminium alloy wing of shaping processability excellence as described belowSheet material, its thickness of slab is below 0.15mm, and by the particle diameter of intermetallic compound, high inclination-angleMaximum length, the average grain diameter of the intragranular subgrain of high inclination-angle etc. of grain is limited in the scope of regulationIn. In addition, in patent documentation 2, disclose as described below resistance to together with (French: avec) property (difficultyCause and the spy who contacts in abutting connection with between fin to produce inhomogeneous distortion during because of expanderProperty), the heat exchanger aluminum alloy fin material of stackability excellence, its thickness of slab is less than 0.11mm, contains ruleQuantitative Fe, Ti, and Si, Cu are limited in below ormal weight, and percentage elongation is limited in to ruleIn fixed scope. In patent documentation 3, disclosing the resistance to heat exchanger together with property excellence as described below usesAluminum alloy fin material, its thickness of slab is less than 0.11mm, and the amount of regulation element is limited in to regulationScope in. In addition, in patent documentation 4, disclose attenuate stretching fin as described below with highStrength aluminium alloy thin plate and manufacture method thereof, the thickness of slab after it is cold rolling is 0.115mm, and will specify unitElement restriction within the limits prescribed.
Formerly technical literature
Patent documentation
Patent documentation 1: TOHKEMY 2006-104488 communique
Patent documentation 2: No. 4275560 communique of Japan Patent
Patent documentation 3: TOHKEMY 2005-126799 communique
Patent documentation 4: Japanese kokai publication sho 64-8240 communique
Brief summary of the invention
The problem that invention will solve
But, in existing fin material, there is following problem.
In described existing technology, realize the raising of processability, but in recent years, except heat exchangeOutside the further miniaturization of device, lightweight, high performance, also expect the more easily fin material of processingSupply, therefore seek the raising of further processability.
In addition, in shaping, exist and produce time and again the situation of breaking that is known as " collar breaks ". ,In the time piercing through with plunging operation, produce small be full of cracks at processing end face, finally open outside thusWhen shaping, becoming collar breaks. In the case of the above-mentioned collar of generation breaks, when making copper pipe pass quiltThe collar hole of the formed products that fin is shaped when this copper pipe is carried out to expander, easily produces stacked looseIt is extremely narrow such, so-called together with phenomenon that the interval of backing becomes. And, according to this together with phenomenon,Exist the flowing resistance of heat exchanger to increase such problem. , there is problem as described below, collarBreak and not only impair the outward appearance of fin, also produce the bad shape of performance reduction as heat exchanger etc.Condition, thus the value as product reduced. Thereby the collar of seeking further to suppress above-mentioned breaksThe exploitation of the fin material of the generation of splitting.
At this, the fin material that patent documentation 1 is recorded has been realized the improvement of resistance to collar disruptiveness. But,Owing to being actively added with Mn, therefore exist because of the amount of Mn and create conditions cause producing thickLarge intermetallic compound or because of solid solution Mn easily processing solidify such problem. Therefore, existImprove the resistance to collar this respect that breaks and also have leeway.
Summary of the invention
The present invention completes in view of described problem points, and its problem is to provide a kind of resistance to collar disruptiveness excellentHeat exchanger aluminum alloy fin material for different attenuate stretching and punching, the fin that it is used with attenuate stretching and punchingMaterial is object, the generation that the collar can suppress to be shaped processing time breaks.
For solving the technical scheme of problem
, attenuate stretching and punching involved in the present invention with heat exchanger aluminum alloy fin material by containingFe:0.010～0.4 quality %, remainder comprise Al and inevitably impurity, Al purity are 99.30More than quality % aluminium alloy forms, and described attenuate stretching and punching is with heat exchanger aluminum alloy fin materialThickness is less than 0.115mm, and the average grain diameter of subgrain is below 2.5 μ m and yield strength is130N/mm2Above. In addition, to exceed the intermetallic compound of 3 μ m be 2000/mm to maximum length2Below.
According to said structure, by adding the Fe of ormal weight, be formed with Al-Fe series intermetallic compound,Or solid solution is in aluminium base, the subgrain when stamping is micronized, solidify thereby suppress processing.In addition, by restriction Al purity, can suppress the increase of intermetallic compound. And, by by AsiaThe average grain diameter of crystal grain is made as below 2.5 μ m, is less than the percentage elongation of the fin material of the thickness of 0.115mmIncrease. In addition, by yield strength is made as to 130N/mm2Above, use as attenuate stretching and punchingFin material and obtain suitable intensity. In addition, by maximum length being exceeded to the intermetallic of 3 μ mCompound is made as 2000/mm2Below, can prevent from leading as starting point because of the intermetallic compound taking thickThe generation that the collar causing breaks.
Attenuate stretching and punching involved in the present invention is characterised in that with heat exchanger aluminum alloy fin material,About the chemical composition of described aluminium alloy, also contain Cu:0.005～0.05 quality %, and suppress for Si:Below 0.15 quality %, Mn: be less than 0.015 quality %, below Cr:0.015 quality %.
According to said structure, by adding the Cu of ormal weight, can guarantee the rigidity after thin-walled property, in addition,By Si, Mn, Cr being suppressed at below ormal weight or being less than ormal weight, can suppress crystal (Intermetallic compound) coarsening.
Attenuate stretching and punching involved in the present invention is characterised in that with heat exchanger aluminum alloy fin material,About the chemical composition of described aluminium alloy, also there is Ti:0.01～0.05 quality %.
According to said structure, by adding the Ti of ormal weight, can make ingot structure miniaturization.
Attenuate stretching and punching involved in the present invention also can be at wing with heat exchanger aluminum alloy fin materialSheet surface possesses surface treatment diaphragm. As surface treatment diaphragm, can enumerate corrosion resistanceDiaphragm, hydrophilic protective films, lubricity diaphragm etc.
According to said structure, can improve corrosion resistance, hydrophily, formability etc. and environment for use,The characteristic that purposes etc. are corresponding.
The manufacture method of heat exchanger aluminum alloy fin material for attenuate stretching and punching involved in the present inventionThe attenuate stretching and punching heat exchanger aluminum alloy fin material that is described record (does not possess surface treatment guarantorCuticula) manufacture method, it is characterized in that heat exchanger aluminium alloy wing for described attenuate stretching and punchingThe manufacture method of sheet material is carried out operation as described below: heat treatment step, and in this heat treatment step,Implement 1 little with the temperature of 450～500 DEG C to thering is the aluminium alloy cast ingot of chemical composition of described aluminium alloyTime more than heat treatment; Hot-rolled process, after described heat treatment, at the end temp of hot finishing is250 DEG C above and be less than under the condition of 300 DEG C and implement hot rolling; Cold working operation, after described hot rolling,Implementing cold working rate is more than 96% cold working; Modified annealing operation, after described cold working,Implement the temperature maintenance modified annealing of 1～6 hour following with 230 DEG C.
According to above-mentioned manufacture method, by heat treatment step, the tissue of ingot casting is homogenized, byHot-rolled process makes heat prolong plate not to be become recrystallized structure and is rolled. Then, by cold working operation andAfter modified annealing, do not produce the coarsening of subgrain and become the thickness that is less than 0.115mm, by tuneMatter annealing operation and make cold working part by modified.
Invention effect
Attenuate stretching and punching involved in the present invention can be suppressed to heat exchanger aluminum alloy fin materialThe collar that shape adds man-hour breaks. Therefore, can prevent from damaging fin outward appearance, produce as heat exchangeThe undesirable conditions such as the performance reduction of device.
In addition, the manufacture of heat exchanger aluminum alloy fin material for attenuate stretching and punching involved in the present inventionMethod can produce the heat exchanger aluminum alloy fin material of resistance to collar disruptiveness excellence.
Detailed description of the invention
Below, to for realizing attenuate stretching and punching heat exchanger aluminium alloy wing involved in the present inventionThe mode of the manufacture method of sheet material (following, to be suitably called fin material) and fin material describes.
<fin material>
Fin material involved in the present invention as the Fe by containing ormal weight, remainder comprise Al andInevitably impurity, Al purity are the attenuate stretching punching that aluminium alloys more than 99.30 quality % formsPress and use. And the thickness of this fin material is less than 0.115mm, the average grain diameter of subgrain is limited in2.5 μ m are following and yield strength is limited in to 130N/mm2Above. In addition, the gold of 3 μ m will be exceededBetween genus, compound is limited in 2000/mm2Below. In addition, about the chemical composition of aluminium alloy, excellentThe Cu that choosing contains ormal weight as required, and in the inevitable impurity that aluminium alloy is comprisedSi, Mn, Cr suppress for ormal weight is following or be less than ormal weight. And then also can be as required andThe Ti that contains ormal weight.
Below, each structure is described, first, chemical composition is described, then to otherStructure describes.
(Fe:0.010～0.4 quality %)
Fe is owing to forming Al-Fe series intermetallic compound (or solid solution is in aluminium base), can make punchingSubgrain when pressing formation is small and contribute to process and solidify the element suppressing, and has the collar of minimizing and breaksThe effect of unfavorable condition. In addition, also have the subgrain that contributes to aluminium alloy plate big or small effect,Put forward high-intensity effect. In the time that Fe amount is less than 0.010 quality %, cannot obtain described effect,Worsen in stamping middle collar disruptiveness. On the other hand, in the time that Fe amount exceedes 0.4 quality %,Form thick intermetallic compound, resistance to collar disruptiveness is poor. Therefore, Fe amount is made as0.010～0.4 quality %.
(Cu:0.005～0.05 quality %)
Further preferably add Cu in order to ensure the rigidity after thin-walled property. Its effect is by adding0.005 quality % obtains above. On the other hand, in the time that Cu amount exceedes 0.05 quality %, leadCause processing and solidify, except reducing resistance to together with property, also cause resistance to collar disruptiveness and corrosion resistanceReduce. Thereby, in the situation that adding Cu in order to ensure rigidity, Cu amount is made as0.005～0.05 quality %. More preferably 0.01～0.05 quality %.
(Si:0.15 quality % following (comprising 0 quality %))
Although Si is the element of sneaking into as inevitable impurity, when Si amount exceedes 0.15When quality %, crystal (intermetallic compound) coarsening, this becomes the stress collection that shaping adds man-hourMid point, and become the starting point of breaking. Thereby, in the situation that containing Si, Si amount is made asBelow 0.15 quality %. It should be noted that, also can suppress to till 0 quality %.
(Mn: be less than 0.015 quality % (comprising 0 quality %))
Although Mn is the element of sneaking into as inevitable impurity, when Mn amount is0.015 quality % is when above, crystal (intermetallic compound) coarsening, and this becomes to be shaped and adds man-hourStress concentration point, and become the starting point of breaking. Thereby, in the situation that containing Mn, by MnAmount suppresses for being less than 0.015 quality %. Further preferably suppress for being less than 0.005 quality %. NeedBe noted that and also can suppress to till 0 quality %.
(Cr:0.015 quality % following (comprising 0 quality %))
Although Cr is the element of sneaking into as inevitable impurity, when Cr amount exceedesWhen 0.015 quality %, crystal (intermetallic compound) coarsening, this becomes shaping and adds answering of man-hourPower centrostigma, and become the starting point of breaking. Thereby, in the situation that containing Cr, by Cr amountInhibition is below 0.015 quality %. It should be noted that, also can suppress to till 0 quality %.
(Ti:0.01～0.05 quality %)
Ti, in order to make ingot structure miniaturization, also can be used as Al-Ti-B intermediate alloy and adds. ,Also can be by the fine agent of Al-Ti-B ingot casting of ratio that is made as Ti:B=5:1 or 5:0.2 with pieceOr the form of rod to motlten metal (plate slab before solidifying to smelting furnace, field trash filter,Motlten metal in any stage that degasser, flow of molten metal amount control device drop into) add,Ti amount is allowed to contain to 0.05 quality %. In the time that Ti amount is less than 0.01 quality %, cannot obtainObtain the effect of ingot structure miniaturization. On the other hand, in the time that Ti amount exceedes 0.05 quality %,Crystal (intermetallic compound) coarsening, this becomes the stress concentration point that shaping adds man-hour, and becomesFor the starting point of breaking. Thereby, in the situation that adding Ti, Ti amount is made as to 0.01～0.05Quality %.
(remainder: Al and inevitably impurity)
The composition of fin material is except above-mentioned element, and remainder comprises Al and inevitably assortedMatter. It should be noted that, as inevitable impurity, except described Si, Mn, Cr,For example, for remelting, aluminium ingot, intermediate alloy comprise, conventionally Mg, the Zn in the scope known,Zr, Ce, Ga, V, Ni etc. are allowed to separately in Al purity is not less than the scope of 99.30 quality %Contain to 0.05 quality %.
(Al purity: more than 99.30 quality %)
In the time that Al purity is less than 99.30 quality %, be accompanied by the increase of intermetallic compound, collar is brokenSplit increase, corrosion resistance reduces. Thereby, more than Al purity is made as to 99.30 quality %.
(thickness: be less than 0.115mm)
The present invention is according to the requirement of the miniaturization of heat exchanger in recent years, lightweight, high performance etc.,From realizing the viewpoint of thin-walled property of fin material, taking the fin material of thickness that is less than 0.115mm as rightResemble. Thereby the thickness of fin material is for being less than 0.115mm.
(average grain diameter of subgrain: 2.5 μ m are following)
In order to realize the increase of percentage elongation of fin material of the thickness that is less than 0.115mm, need to be by alloyIn the average grain diameter of subgrain be made as below 2.5 μ m. When the average grain diameter of subgrain exceedes 2.5 μ mTime, cannot obtain fully the percentage elongation of fin material. Thereby, the average grain diameter of subgrain is made asBelow 2.5 μ m. It should be noted that, lower limit does not limit especially, can be also 0 μ m (,Also can not contain subgrain). By being made as above-mentioned scope, even if utilizing solid solution Mn, solid solutionCu etc. process in curing situation, also can suppress the generation that collar breaks.
Then, the assay method of the number of the average grain diameter to subgrain and intermetallic compound is saidBright.
First, utilize EBSD (ElectronBackScatteredDiffractionPattern) method to sweepingRetouch electron microscope (SEM:ScanningElectronMicroscopy-Electron) the tissue side of carrying outResolve position. EBSD normal direction sample irradiates electric wire, and utilizes the reflection electronic Kikuchi lines now producingDiffraction is determined crystal orientation. In addition, crystal orientation is resolved and can be used for example OIM processed of TSL society(OrientationImagingMicroscopy.TM)。
Then, the average grain diameter of subgrain is to calculate crystal grain according to this SEM/EBSD determination dataQuantity, and by the quantity of crystal grain the whole area divided by fin material, by near the area of each crystal grainBe similar to the average grain diameter that diameter in round situation is defined as subgrain.
It should be noted that, the average grain diameter of subgrain and the number of intermetallic compound can be by compositionsComposition, described later creating conditions are controlled. Particularly, the average grain diameter of subgrain is by each compositionAmount, the heat-treat condition that homogenizes (temperature and time), hot finishing end temp, cold workingRate, modified annealing conditions (temperature and time) are controlled, and the number of intermetallic compound is by each one-tenthAmount, the heat-treat condition that homogenizes (temperature and time) etc. of dividing are controlled.
(yield strength: 130N/mm2Above)
Fin material of the present invention, as attenuate stretching and punching use, is therefore made as yield strength130N/mm2Above. When yield strength is less than 130N/mm2Time, undercapacity, draws when carrying out attenuateStretch and produce collar when stamping and break. Thereby, yield strength is made as to 130N/mm2Above. NeedBe noted that and preferably exceed 130N/mm2. In addition, in the time that intensity is too high, owing to subtractingWhen thin stretching and punching is shaped, easily produce collar and break, therefore preferably higher limit is made as to 170N/mm2。
For example, cut out based on No. JIS5 in the draw direction mode parallel with rolling direction from fin materialTensile sample, by implementing the tension test based on JISZ2241, can carry out yield strength thusMensuration.
It should be noted that the number of average grain diameter, yield strength and the intermetallic compound of subgrainCan be grouped into by one-tenth, described later creating conditions control. Particularly, the average particle of subgrainTemperature is finished by the amount of each composition, the heat-treat condition that homogenizes (temperature and time), hot finishing in footpathDegree, cold working rate, modified annealing conditions (temperature and time) etc. is controlled, and yield strength is by respectivelyThe amount of composition, the heat-treat condition that homogenizes (temperature and time), modified annealing conditions (temperatureWith the time) etc. control. The number of intermetallic compound is by amount, the homogeneous heat-transmission of each compositionTreatment conditions (temperature and time) etc. are controlled.
Fin material involved in the present invention also can possess surface treatment diaphragm in wing sheet surface. NeedBe noted that wing sheet surface represents the single or double of fin material.
(surface treatment diaphragm)
As surface treatment diaphragm, according to environment for use, purposes, enumerate and transform diaphragm, resinDiaphragm, inorganic protective film, also can combine said protection film and (on conversion diaphragm, resin is setDiaphragm, inorganic protective film). In addition, as resin protection film, inorganic protective film, enumerate corrosion resistantErosion property resin protection film, hydrophilic resin diaphragm, hydrophilic inorganic diaphragm, lubricity resin are protectedCuticula etc., also can suitably combine said protection film.
As transforming diaphragm, enumerate for example chromium phosphate hydrochlorate. As corrosion-resistant resin diaphragm,Enumerate the resins such as epoxies, polyurethanes, acrylic compounds, polyesters, its thickness is preferably 0.5～5 μ m.As hydrophilic protective films, enumerate waterglass class inorganic matter, contain polyacrylic acid or polyacrylateSuch resin, contain sulfonic group or the such resin of sulfonic group inductor etc., its thickness is preferably0.05～10 μ m. Enumerate resin that contains PPG etc. as lubricity resin protection film, itsThickness is preferably 0.1～10 μ m.
Combination corrosion-resistant resin diaphragm, hydrophilic resin diaphragm, hydrophilic inorganic diaphragm,In two or more situation in lubricity resin protection film, preferably at corrosion-resistant resin diaphragmUpper surface one side is provided with hydrophilic resin diaphragm, protects at hydrophilic resin diaphragm, hydrophilic inorganicThe face side of cuticula is provided with lubricity resin protection film.
The manufacture method of<fin material>
The manufacture method of fin material involved in the present invention is the manufacture method of described fin material, carries outHeat treatment step, hot-rolled process, cold working operation, modified annealing operation. And then as required, alsoCan comprise ingot casting production process, surface treatment procedure.
Below, each operation is described.
(ingot casting forming process)
Ingot casting forming process is by aluminium alloy smelting, casting and the operation of making aluminium alloy cast ingot.
In ingot casting forming process, utilization forms the aluminium alloy smelting with described chemical compositionMotlten metal, makes the ingot casting of regulation shape. The method of aluminium alloy smelting, casting is not specialGround limits, and uses existing known method. For example, can use vacuum induced stove and meltRefining, and use continuous casting process, semi-continuous casting method and cast.
(heat treatment step)
Heat treatment step be the chemical composition to thering is described aluminium alloy aluminium alloy cast ingot withThe temperature of 450～500 DEG C is implemented the operation of above heat treatment (heat treatment homogenizes) in 1 hour.
In the time that heat treatment temperature is less than 450 DEG C, homogenizing of the tissue of ingot casting becomes insufficient. In addition,Cause the reduction of processability between heat. Make in addition yield strength be formed as being less than lower limit. On the other hand,In the time that heat treatment temperature exceedes 500 DEG C, adding between the minute metallic of hankering carrying out miniaturization, compound is thickLargeization, subgrain coarsening and make percentage elongation reduce. In addition, cause the increase of solid solution capacity. Thereby,Heat treatment temperature is made as to 450～500 DEG C. In addition, heat treatment needs only 1 hour retention time above justCan obtain described effect, therefore without set upper limit especially. On the other hand, little owing to exceeding 10Time effect is saturated, therefore from the angle of economy, heat treatment time be preferably 24 times withIn.
(hot-rolled process)
Hot-rolled process is taking the end temp of hot finishing as more than 250 DEG C and little after described heat treatmentImplement the operation of hot rolling in the conditions of 300 DEG C.
In the time that the end temp of hot finishing is less than 250 DEG C, the calenderability of material reduces, and calendering itself becomesMust be difficult, thus make thickness of slab be difficult to control, and productivity reduces. On the other hand, when the end of hot finishingTemperature is when more than 300 DEG C, in order to form recrystallized structure at hot Yan Banchu, raw afterwards in modified annealingBecome fibrous identical crystal orientation group, produce necking down while wearing with plunging operation perverse. In addition,It is large that subgrain diameter becomes, and also makes yield strength be formed as being less than lower limit. Thereby, by the knot of hot finishingShu Wendu is made as 250 DEG C above and is less than 300 DEG C. More preferably 260～290 DEG C.
(cold working operation)
Cold working operation is that after described hot rolling, to implement cold working rate be that more than 96% cold working is (coldRoll) operation.
After hot rolling finishes, carry out one or many cold working, thereby fin material is made as desirableFinal thickness of slab. But in the time that cold working rate is less than 96%, subgrain is coarsening after modified annealing.In addition, yield strength reduces. Thereby, the cold working rate in cold working is made as more than 96%. At this,Cold worked, carry out intermediate annealing midway in the situation that, cold working rate is until from intermediate annealingWorking modulus till soleplate is thick. Therefore,, in the time carrying out intermediate annealing, be difficult to reach more than 96% coldWorking modulus, does not therefore carry out intermediate annealing. It should be noted that, cold working rate is preferably more high better,Therefore there is no capping especially.
(modified annealing operation)
Modified annealing operation is to implement to keep 1～6 with the temperature below 230 DEG C after described cold workingHour the operation of modified annealing (final annealing).
In the time that the temperature of modified annealing exceedes 230 DEG C, promote processing to solidify by attenuate stretch processBreak and produce. In addition, yield strength reduces. Thereby, the temperature of modified annealing is made as to 230 DEG CBelow. Be preferably and be less than 180 DEG C. It should be noted that, lower limit does not have regulation especially, butIn order to bring into play the effect of modified annealing, preferably carry out above at 100 DEG C. It should be noted that, modifiedAnnealing is carried out more than 1 hour conventionally, but owing to exceeding 6 hours, effect is saturated, the therefore retention timeIt was 1～6 time.
(surface treatment procedure)
Surface treatment procedure is that the fin material after modified annealing is implemented to surface-treated operation.
In surface treatment procedure, in the situation that forming conversion diaphragm, can be common by usingCoating-type or the conversion processing of the medicament of response type carry out. Forming corrosion-resistant resin protectionIn the situation of the resin protection films such as film, hydrophilic resin diaphragm, lubricity resin protection film, canBy the coating with roll coater, be dried to carry out.
It should be noted that, when carrying out time of the present invention, described each operation is not being caused to negative effectIn scope, also can be between described each operation or front and back comprise other operations. For example, also can wrapContaining the foreign matter of removing the foreign matters such as dust remove operation, face cutting process to the cutting of ingot casting enforcement face,After modified annealing operation, surface treatment procedure, suitably implementing necessary machinery as fin material addsThe machining operation of work etc.
The forming process of the fin material utilization of then, so manufacturing based on attenuate stretching mode and being formed addsWork.
Perforation in the first operation, is implemented in attenuate stretch forming (attenuate stretching and punching) and reaming processing is (perverseWear and plunging is shaped), in the second operation and the 3rd operation, implement attenuate stretch process, theIn four operations, implement outer Zhang Jiagong. And, the resistance to collar disruptiveness excellence of fin material of the present invention, because ofThis can suppress to add based on the shaping of attenuate stretching mode the generation that the collar in man-hour breaks.
Embodiment
Above, to being illustrated for implementing mode of the present invention, below by sending out with discontented unabridged versionThe comparative example of bright main points contrasts and the embodiment that confirmed effect of the present invention is carried out specificallyExplanation. It should be noted that, the present invention is not limited to this embodiment.
[for sample production]
(embodiment No.1～10, comparative example No.11～21)
The aluminium alloy smelting of the composition shown in table 1, casting are formed as to ingot casting, real to this ingot castingAfter executing face cutting, implement the heat treatment that homogenizes of 4 hours with 480 DEG C. With the end temperature of hot finishingSpend the ingot casting becoming after the mode of 270 DEG C homogenizes to this and control and implement hot rolling, thereby formThickness of slab is the hot rolled plate of 3.0mm. In addition, real with the cold working rate of 97.0% or 97.3% left and right respectivelyExecute cold rolling and thickness of slab is made as to 90 μ m and 80 μ m, when then implementing the temperature shown in table 1 and keepingBetween modified annealing and be formed as fin material.
(embodiment No.22～27, comparative example No.28～34)
By the aluminium alloy shown in table 2 (alloy A, B, the C corresponding with table 1) melting, casting and shapeBecome ingot casting, after to this ingot casting enforcement face cutting, implement to homogenize heat treatment, hot rolling, therebyBe formed as the hot rolled plate that thickness of slab is 3.0mm. In addition, except No.34, respectively with 97.0% orThe cold working rate of 97.3% left and right is implemented cold rolling and thickness of slab is made as to 90 μ m and 80 μ m, then implements to adjustMatter is annealed and is formed as fin material. Cold working rate to the thickness of slab hot rolling as 3.0mm of No.34 taking 50%Plate is implemented cold rolling, then uses batch-type furnace and implements the intermediate annealing of 360 DEG C × 3h. Then also distinguishImplement cold rolling and thickness of slab be made as to 90 μ m and 80 μ m with the cold working rate of 94.0% or 94.7% left and right,Then implement modified annealing and become fin material. End temp, the tune of heat treatment, hot finishing homogenizeThe condition of matter annealing is as shown in table 2. It should be noted that, No.30 cannot manufacture fin material.
(embodiment No.35～38, comparative example No.39～42)
No.35 to the fin material as identical with the No.22 of table 2 and No.36, conduct and table 2The No.37 of the identical fin material of No.27 and No.38, as the wing identical with the No.29 of table 2The No.39 of sheet material and No.40, as No.41 and the No.42 of the fin material identical with the No.32 of table 2Carry out following surface treatment (No.1～4).
No.1: the surface of the condition identical with the comparative example 1 of TOHKEMY 2010-223520 communiqueProcess (possessing successively the diaphragm of conversion, hydrophilic protective films, lubricity diaphragm)
No.2: the surface of the condition identical with the embodiment 1 of No. 3383914 communique of Japan PatentReason (possessing successively the diaphragm of conversion, hydrophilic protective films, lubricity resin protection film)
No.3: the surface of the condition identical with the embodiment 1 of TOHKEMY 2008-224204 communiqueProcess (possessing successively the diaphragm of conversion, corrosion-resistant resin diaphragm, hydrophilic protective films)
No.4: the surface of the condition identical with the comparative example 21 of TOHKEMY 2010-223514 communiqueProcess (possessing successively the diaphragm of conversion, corrosion-resistant resin diaphragm)
Table 1 is expressed as being grouped into, and table 2,3 represents to create conditions. It should be noted that, in table,Discontented unabridged version scope of invention, drawn underscore and represented at its numerical value, do not contain composition by "-"Represent. It should be noted that, No.30 cannot produce fin material, therefore in modified annealing one hurdle noteDo "-". In addition, No.16 is based on according to the aluminum alloy fin material (table 2 of the record of patent documentation 1Example 1 (wherein, heat is prolonged thickness of slab (3.5mm) and the modified annealing after end temp, hot rollingTemperature difference)), No.13 is based on according to the aluminum alloy fin material (table 1 of the record of patent documentation 2Example 4 (wherein, processing mode (stretch process) difference)). In addition, No.17 is based on rootAccording to the aluminum alloy fin material (example 3 of table 1) of the record of patent documentation 3, No.33 is based on basisThe aluminum alloy fin material of the record of the patent documentation 4 (example 11 of the table 2 (plate after wherein, cold rollingThick (0.115mm is thick) difference)).
Then,, as the tissue morphology of fin material, utilize the average grain diameter of following method to subgrainAnd the number of 3 more than μ m intermetallic compounds is measured. In addition, utilize following method to by forceDegree and percentage elongation are measured.
[average grain diameter of subgrain]
Utilize EBSD method taking measuring interval as 0.10 μ m to taking observe multiplying power as 1000 times take samplesSEM (SEM) tissue on surface carries out orientation parsing, the number of resolving based on this orientationAccording to carrying out on the OIM processed of TSL society (OrientationImagingMicroscopy.TM) software certainlyMoving calculating, calculates the average grain diameter of subgrain thus. , by measuring number according to SEM/EBSDWhole area according to the quantity of the crystal grain calculating divided by fin material, by making, the area of each crystal grain is nearBe similar to the average grain diameter that diameter in round situation is defined as subgrain. It should be noted that, by adjacencyThe crystal grain that the grain boundary of gun parallax between crystal grain in 2 ° impales is as a crystal grain,Calculate thus the quantity of crystal grain.
[exceeding the number of the intermetallic compound of 3 μ m]
To taking observe multiplying power as 500 times and to area as 1.0mm2Sweeping of taking of specimen surfaceRetouch electron microscope (SEM) tissue and carry out image analysis, calculate thus size and exceed 3 μ m'sCompound quantity. It should be noted that, the size of compound refers to the maximum length of each compound.
[intensity and percentage elongation]
Cut out the stretching based on No. JIS5 from fin material in the draw direction mode parallel with rolling directionTest film. This test film is implemented to the tension test based on JISZ2241, and to hot strength, 0.2%Yield strength and percentage elongation are measured. It should be noted that the evaluation of the present embodiment and comparative exampleIn draw speed carry out with 5mm/min.
[evaluation]
Stamping to the fin material enforcement being shaped by attenuate stretch forming, thus resistance to collar is brokenProperty is evaluated.
The evaluation of resistance to collar disruptiveness is to break to punching press by what produced in collar portion by visualizationFormed products 400 holes are calculated and are evaluated.
" break number/400 × 100 (%) " is made as to generation rate, by generation rate be less than 3% be made as (◎),Be more than 3% by generation rate and be less than 5% less than being made as (zero), being more than 5% to be made as (×) by generation rate.And, among 90 μ m and 80 μ m whole by (◎), that (zero) is all made as is qualified.
Table 1～3 represent measurement result and evaluation result. It should be noted that, in table, discontented unabridged versionScope of invention, draw underscore and represented at its numerical value, cannot be complete because manufacturing fin materialOne-tenth is measured and is evaluated, and is represented by "-".
Table 1
Table 2
Table 3
(based on the evaluation of composition)
As shown in table 1, meet scope of the present invention as No.1～10 of embodiment, therefore resistance to collarDisruptiveness excellence.
On the other hand, the discontented unabridged version scope of invention in No.11～21 as a comparative example, therefore form withUnder result.
In No.11, because Si amount exceedes higher limit, therefore thick intermetallic compound increases,And impair resistance to collar disruptiveness.
In No.12, because Fe amount is less than lower limit, therefore subgrain diameter becomes large, and damagesIn resistance to collar disruptiveness. In No.13, because Fe amount exceedes higher limit, and because Al is pureDegree is less than lower limit, and therefore thick intermetallic compound increases, and impairs resistance to collar disruptiveness.In No.14, because Al purity is less than lower limit, therefore thick intermetallic compound increases, and hasDamage in resistance to collar disruptiveness.
In No.15, because Cu amount exceedes higher limit, therefore cause processing to be solidified, and impairResistance to collar disruptiveness. In No.16, because Mn amount exceedes higher limit, therefore thick metalBetween compound increase, and impair resistance to collar disruptiveness. In No.17, because Mn amount exceedesHigher limit, therefore thick intermetallic compound increases, and because the temperature of modified annealing exceedesLimit value, therefore promotes processing to solidify, and yield strength is formed as being less than lower limit in addition, and impairs resistance toCollar disruptiveness.
In No.18, because Cr amount exceedes higher limit, therefore thick intermetallic compound increases,And impair resistance to collar disruptiveness. In No.19, because Ti amount exceedes higher limit, therefore thickIntermetallic compound increase, and impair resistance to collar disruptiveness. In No.20, due to Ti amountExceed higher limit, therefore thick intermetallic compound increases, and impairs resistance to collar disruptiveness.In No.21, because Fe amount exceedes higher limit, therefore thick intermetallic compound increases, andImpair resistance to collar disruptiveness.
(based on the evaluation of manufacture method)
As shown in table 2, meet scope of the present invention as No.22～27 of embodiment, therefore resistance to cardCircle disruptiveness excellence.
On the other hand, the discontented unabridged version scope of invention in No.28～34 as a comparative example, therefore formsFollowing result.
In No.28, because the heat treated temperature that homogenizes is less than lower limit, therefore homogenize insufficient,And yield strength is formed as being less than lower limit, and impairs resistance to collar disruptiveness. In No.29, byExceed higher limit in the heat treated temperature that homogenizes, therefore subgrain diameter becomes large, and impairs resistance to cardCircle disruptiveness.
In No.30, because the end temp of hot finishing is less than lower limit, therefore calendering itself becomes tiredDifficulty, and cannot manufacture fin material. In No.31, because the end temp of hot finishing exceedes higher limit,Therefore subgrain diameter becomes large, and yield strength is formed as being less than lower limit, and impairs resistance to collarDisruptiveness. In No.32, because modified annealing temperature exceedes higher limit, therefore promote processing to solidify,And yield strength is formed as being less than lower limit, and impairs resistance to collar disruptiveness.
In No.33, because the heat treated temperature that homogenizes exceedes higher limit, therefore subgrain diameter becomesImpair resistance to collar disruptiveness greatly. In No.34, owing to having carried out intermediate annealing, therefore cold addingWork rate is formed as being less than lower limit. Therefore, the average grain diameter of subgrain exceedes higher limit, and surrenderIntensity is formed as being less than lower limit, and impairs resistance to collar disruptiveness.
(having implemented the evaluation of surface-treated situation)
The resistance to collar disruptiveness of the surface-treated fin material in No.35～42 and enforcement table are not implementedThe fin material of face processing is formed as identical result.
It should be noted that, No.16,13,17,33 fin material be assumed to respectively patent documentation 1,The existing aluminum alloy fin material that patent documentation 2, patent documentation 3, patent documentation 4 are recorded. AsIn the present embodiment, above-mentioned existing aluminum alloy fin material does not meet in described evaluationCertain level. Thereby according to the present embodiment, objectively, attenuate involved in the present invention stretchesPunching press is apparent with heat exchanger aluminum alloy fin material than existing aluminum alloy fin material excellence.

Claims (5)

1. a heat exchanger aluminum alloy fin material for attenuate stretching and punching, is characterized in that,
Described attenuate stretching and punching with heat exchanger aluminum alloy fin material by containing Fe:0.010～0.4 matterAmount %, suppress for Mn: be less than 0.015 quality %, remainder comprises Al and inevitably assortedMatter, Al purity are that aluminium alloys more than 99.30 quality % forms,
Described attenuate stretching and punching is less than 0.115mm, Asia with the thickness of heat exchanger aluminum alloy fin materialThe average grain diameter of crystal grain is below 2.5 μ m and yield strength is 130N/mm2Above,
The intermetallic compound that exceedes 3 μ m is limited in to 2000/mm2Below.
2. heat exchanger aluminum alloy fin material for attenuate stretching and punching according to claim 1, itsBe characterised in that,
About the chemical composition of described aluminium alloy, also contain Cu:0.005～0.05 quality %, and suppressBelow Si:0.15 quality %, below Cr:0.015 quality %.
3. heat exchanger aluminum alloy fin material for attenuate stretching and punching according to claim 1, itsBe characterised in that,
About the chemical composition of described aluminium alloy, also contain Ti:0.01～0.05 quality %.
4. heat exchanger aluminum alloy fin material for attenuate stretching and punching according to claim 1, itsBe characterised in that,
Possesses surface treatment diaphragm in wing sheet surface.
5. in a claims 1 to 3, the attenuate stretching and punching described in any one closes with heat exchanger aluminiumThe manufacture method of greenfinch sheet material, is characterized in that,
This manufacture method is carried out operation as described below:
Heat treatment step, in this heat treatment step, with the temperature of 450～500 DEG C to thering is described aluminiumThe aluminium alloy cast ingot of the chemical composition of alloy is implemented above heat treatment in 1 hour;
Hot-rolled process, after described heat treatment, the end temp of hot finishing be more than 250 DEG C andBe less than under the condition of 300 DEG C and implement hot rolling;
Cold working operation, after described hot rolling, implementing cold working rate is more than 96% cold working;
Modified annealing operation, after described cold working, implements to keep 1～6 with 200 DEG C of following temperatureHour modified annealing.
CN201280015567.5A 2011-03-31 2012-03-06 Heat exchanger aluminum alloy fin material and manufacture method thereof for attenuate stretching and punching Active CN103459629B (en)

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JP2011080855A JP5828657B2 (en) 2011-03-31 2011-03-31 Aluminum alloy fin material for heat exchanger
JP2011080853A JP5843462B2 (en) 2011-03-31 2011-03-31 Aluminum alloy fin material for heat exchanger for drawless press
JP2011-080853 2011-03-31
PCT/JP2012/055659 WO2012132784A1 (en) 2011-03-31 2012-03-06 Drawless press aluminium alloy fin material for heat exchanger, and manufacturing method for same

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JP4257649B2 (en) 2003-10-27 2009-04-22 三菱アルミニウム株式会社 Aluminum alloy fin material for heat exchangers with excellent Abeck resistance
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JP2009250510A (en) * 2008-04-04 2009-10-29 Mitsubishi Electric Corp Heat exchanger and its manufacturing method
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