CN104685082B - Combination (-type)press heat exchanger aluminum alloy fin material and its manufacture method - Google Patents
Combination (-type)press heat exchanger aluminum alloy fin material and its manufacture method Download PDFInfo
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- CN104685082B CN104685082B CN201380051304.4A CN201380051304A CN104685082B CN 104685082 B CN104685082 B CN 104685082B CN 201380051304 A CN201380051304 A CN 201380051304A CN 104685082 B CN104685082 B CN 104685082B
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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
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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
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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
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Abstract
The present invention provides a kind of combination (-type)press heat exchanger aluminum alloy fin material and its manufacture method, and the combination (-type)press heat exchanger aluminum alloy fin material is characterised by that be made up of aluminium alloy, the aluminium alloy contains Fe：0.010～0.4 mass %, Cu：0.005～0.05 mass %, surplus is made up of Al and inevitable impurity, Al purity is more than 99.30 mass %, the thickness of slab of the combination (-type)press heat exchanger aluminum alloy fin material is less than 0.115mm, the mean diameter of subgrain is less than 2.5 μm, and yield strength is higher than 130MPa and 155MPa.Can obtain that resistance to aperture is anti-thread breakage and the excellent combination (-type)press heat exchanger aluminum alloy fin material of treatability.Can obtain suppressing the resistance to aperture of the generation of aperture crackle when forming anti-thread breakage and excellent corrosion resistance heat exchanger aluminum alloy fin material.
Description
Technical field
The present invention relates to be used for the combination (-type)press heat exchanger aluminum alloy fin material and its manufacture method of heat exchanger.
Background technology
In recent years, it is (below, suitable to be referred to as with aluminum alloy fin material in the heat exchanger of the heat exchanger for air-conditioner etc.
Fin material) in, Chlorofluorocarbons (CFCs) and the conversion to new refrigerant are limited due to following, and miniaturization, the lightweight of air-conditioner itself
Or high performance etc., also pursue all the more thin-walled property, thickness of slab reaches below 0.15mm, recently then thin-walled property to 0.09mm or so.
Here, the manufacturing process of fin material has stretching (draw) mode, non-stretching (drawless) mode and stretching-Fei La
Stretch complex method (compound mode).Stretching mode (rushes edge by the operation that swells, drawing sequence, punching (perforation) and reaming operation：
Burring), enlarging (reflaring) operation is constituted again, and non-stretching mode is by punching and reaming operation, (the thinning drawing of thinning drawing
It is deep) operation, again enlarging operation composition, compound mode is mainly by the operation that swells, drawing sequence, punching and reaming operation, thinning drawing
Deep operation, again enlarging operation are constituted.
The exploitation of the fin material in the 1970's it is initial, among 3 above-mentioned manufacturing process, use stretching side
Formula, has used the soft aluminium alloy having excellent formability that swells.Thereafter, in order to tackle the trend of thin-walled property, high intensity, and increase
The employing of non-stretching mode is added, to reduce hot glue during thinning drawing processing, begin to use the hard containing Mn
Aluminium alloy.Followed by, the abolishment cleaned from the organic solvent of environmental problem research press oil, by cleaning
Volatility punching oil using increasing, precoat affecting using expanding etc. for fin material, stretching-non-stretching complex method (combination
Mode) it is used, even if thin-walled, the exploitation propulsion of the still excellent various aluminium alloys of intensity and formability.
No matter in which kind of manufacturing process, the perforation ＆ for shaping the effective aperture of copper pipe rush edge shaping and enlarging again into
Shape, is all necessary and integral forming process for fin material.But, these shaping for thickness of slab by thin-walled property extremely
For the fin material of below 0.15mm, become severe cruel shaping.For this purpose, thin-walled property as correspondence, will develop processability of sening as an envoy to
The fin material of raising.
For example, Patent Document 1 discloses a kind of excellent aluminum alloy fin material of shaping processability, its thickness of slab is 0.15mm
Hereinafter, the set particle diameter of intermetallic compound, the greatest length of wide-angle crystal grain, subgrain in wide-angle crystal grain it is average
Particle diameter etc..In addition, Patent Document 2 discloses the excellent heat exchanger of a kind of resistance to adhesion (avec) property, stackability being closed with aluminum
Greenfinch sheet material, its thickness of slab are less than 0.11mm, and given amount contains Fe, Ti, Si, Cu are limited to below given amount, and set
Elongation percentage.A kind of excellent heat exchanger aluminum alloy fin material of resistance to adhesive is Patent Document 3 discloses, its thickness of slab is less than
0.11mm, the content of set regulation element.In addition, Patent Document 4 discloses it is a kind of it is cold rolling after thickness of slab be
0.115mm, non-stretching fin high-strength aluminum alloy thin plate and its manufacture method of set regulation element.
Prior art literature
Patent documentation
Patent documentation 1：Japanese Unexamined Patent Publication 2006-104488 publications
Patent documentation 2：No. 4275560 publications of Japanese Patent No.
Patent documentation 3：Japanese Unexamined Patent Publication 2005-126799 publications
Patent documentation 4：Japanese Unexamined Patent Application 64-8240 publication
Invent problem to be solved
However, in existing fin material, still having following such problem.
In the existing technology, although the raising of achievable processability, but in recent years, except expecting heat exchanger
Further beyond miniaturization, lightweight and high performance, also it is desirable to the fin material that supply is easily processed, processability is thus required
Further raising.In addition, with the thin-walled property of former material, fin material is easily deformed during process, therefore also require that carrying for treatability
It is high.
In addition, can usually be referred to as the crackle of aperture crackle in shaping.That is, bore a hole when ＆ rushes edge operation and processing end
There is fine cracking in face, thus cause to become aperture crackle when finally enlarging shapes again.When such aperture crackle occurs,
All neck ring holes (collar hole) of the formed products in finned blade forming by copper pipe and when carrying out expander to the copper pipe, stacking
The interval of fin become extremely narrow, be susceptible to so-called adhesion phenomenon.Also, due to this adhesion phenomenon, can there is heat exchange
The problem of the flowing resistance increase of device.That is, aperture crackle not only damages the outward appearance of fin, and can produce as heat exchanger
A problem that performance is reduced, has problem as making to reduce as the value of product.It is therefore desirable to develop can be further
The fin material of the generation of aperture crackle as suppressing.
Here, the fin material described in patent documentation 1 realizes the anti-thread breakage improvement in resistance to aperture.But, because actively adding Mn,
So according to the content and manufacturing condition of Mn, cause the presence of thick intermetallic compound, or it is easy because of solid solution Mn
Problem as generation processing hardening.Therefore, the crackle of resistance to aperture improves still leeway.
The content of the invention
The present invention in view of the problem points and formed, its problem is, there is provided a kind of fin material with combination (-type)press is
Object, can suppress the combination (-type)press that resistance to aperture is anti-thread breakage and treatability is excellent of the generation of aperture crackle when forming to use
Heat exchanger aluminum alloy fin material.
Means for solving the problems
That is, combination (-type)press heat exchanger aluminum alloy fin material of the invention is characterised by, is made up of aluminium alloy
Combination (-type)press heat exchanger aluminum alloy fin material, the aluminium alloy contains Fe：0.010～0.4 mass %, Cu：0.005
～0.05 mass %, surplus are made up of Al and inevitable impurity, and Al purity is more than 99.30 mass %, the joint pressure
The thickness of slab of machine heat exchanger aluminum alloy fin material is less than 0.115mm, and the mean diameter of subgrain is less than 2.5 μm, and
Yield strength is more than 130MPa and below 155MPa.
According to such composition, by adding Fe with ormal weight, Al-Fe series intermetallic compounds can be formed, or which is in aluminum
Solid solution in matrix, subgrain during extrusion molding obtain miniaturization, and processing hardening is suppressed.Additionally by being added with ormal weight
Cu, treatability during thin-walled property are ensured that.Additionally by regulation Al purity, the increase of intermetallic compound is suppressed.Also, it is logical
Crossing makes the mean diameter of subgrain below 2.5 μm, and the elongation percentage of the fin material of the thickness of slab less than 0.115mm increases.In addition, logical
Crossing makes yield strength more than 130MPa and below 155MPa, and the reduction of the treatability come with thin-walled property is suppressed.
The combination (-type)press heat exchanger aluminum alloy fin material of the present invention is characterised by, with regard to the change of the aluminium alloy
Study point, be suppressed to Si：Less than 0.20 mass %, Mn：Less than 0.015 mass %, Cr：Below 0.015 mass %.
According to such composition, by Si, Mn, Cr are suppressed to below ormal weight or less than ormal weight, crystal is (i.e. golden
Compound between category) coarsening be suppressed.
The combination (-type)press heat exchanger aluminum alloy fin material of the present invention is characterised by, with regard to the change of the aluminium alloy
Study point, also contain Ti：0.01～0.05 mass %.
According to such composition, by adding Ti with ormal weight, ingot bar tissue is micronized.
The combination (-type)press heat exchanger aluminum alloy fin material of the present invention can also possess at surface in wing sheet surface
Reason epithelium.As surface treatment epithelium, corrosion resistance epithelium, hydrophilic epithelium and lubricity epithelium etc. can be enumerated.
According to such composition, the spy of the correspondence use environment and purposes etc. such as corrosion resistance, hydrophilic, formability can be made
Property improve.
The manufacture method of the combination (-type)press heat exchanger aluminum alloy fin material of the present invention is the joint pressure of above-mentioned record
The manufacture method of machine heat exchanger aluminum alloy fin material (not possessing the fin material of surface treatment epithelium), it is characterised in that
Carry out following operation：For the aluminium alloy ingot bar of the chemical composition with the aluminium alloy, implement 1 with 450～500 DEG C of temperature
The heat treatment step of the heat treatment more than hour；It is after the heat treatment, as more than 250 DEG C and low with the end temp of hot finish to gauge
Implement the hot-rolled process of hot rolling in 300 DEG C of conditions；After the hot rolling, implement the cold worked cold of cold working rate more than 96%
Manufacturing procedure；After the cold working, the quenched of quenched annealing for implementing to be kept for 1～6 hour with 135～210 DEG C of temperature is moved back
Firer's sequence.
According to such manufacture method, by heat treatment step, the tissue of ingot bar is homogenized, by hot-rolled process,
Recrystallized structure will not be formed in hot rolled plate and be rolled.Then, by cold working operation, Asia will not after quenched annealing, be made
The coarsening of crystal grain occurs, and becomes the thickness of slab less than 0.115mm, gives elongation percentage by quenched annealing operation, and promotes subgrain
Miniaturization.
Invention effect
The combination (-type)press heat exchanger aluminum alloy fin material of the present invention can suppress aperture crackle when forming,
Improve treatability.Therefore, it is possible to prevent damage fin outward appearance, and as heat exchanger performance reduce etc. bad feelings
Condition.
In addition, the manufacture method of the combination (-type)press heat exchanger aluminum alloy fin material of the present invention, can manufacture resistance to hole
Mouthful anti-thread breakage and excellent heat exchanger aluminum alloy fin material of treatability.
Description of the drawings
Fig. 1 is for illustrating (a) axonometric chart of the evaluation methodology of treatability and (b) side view.
Specific embodiment
Hereinafter, it is (below, suitable to claim for the combination (-type)press heat exchanger aluminum alloy fin material for realizing the present invention
For fin material) and the mode of manufacture method of fin material illustrate.
<Fin material>
The fin material of the present invention, is the fin material as combination (-type)press being made up of aluminium alloy, and the aluminium alloy is advising
Quantitatively contain Fe and Cu, surplus is made up of Al and inevitable impurity, Al purity is more than 99.30 mass %.And, the wing
The thickness of slab of sheet material is less than 0.115mm, and the mean diameter of subgrain is defined as less than 2.5 μm, and yield strength is defined as being more than
130MPa and below 155MPa.In addition, among inevitable impurity contained by aluminium alloy, Si, Mn, Cr are suppressed to rule preferably
Below quantitative or less than ormal weight.Additionally, as needed can also the Ti containing ormal weight.
Hereinafter, for each composition, first chemical composition is illustrated, again other compositions is illustrated afterwards.
(Fe：0.010～0.4 mass %)
Fe forms Al-Fe series intermetallic compounds (or solid solution in aluminum substrate), can make subgrain during extrusion molding
It is fine, therefore contribute to suppress the element of processing hardening, the effect bad with aperture crackle is reduced.In addition, also with right
The size of the subgrain of aluminium alloy plate plays the effect of help, makes the effect of intensity raising.Fe contents are less than 0.010 mass %
When, effect that cannot be described, the anti-thread breakage difference in resistance to aperture in extrusion molding, in addition, yield strength becomes too low and treatability is poor.
On the other hand, if being higher than 0.4 mass %, thick intermetallic compound formed, the anti-thread breakage difference in resistance to aperture.Therefore, Fe contents
For 0.010～0.4 mass %.
(Cu：0.005～0.05 mass %)
In order to ensure treatability during thin-walled property, further add Cu.Its effect is by more than 0.005 mass % of addition
Can obtain.On the other hand, if Cu contents are higher than 0.05 mass %, cause processing hardening, except reduce resistance to adhesive with
Outward, also cause the anti-thread breakage reduction with corrosion resistance in resistance to aperture.Therefore, Cu contents are 0.005～0.05 mass %.More preferably
0.01～0.05 mass %.
(Si：Less than 0.20 mass % (containing 0 mass %))
Si is the element being mixed into as inevitable impurity, if Si contents reach more than 0.20 mass %, crystal
(intermetallic compound) coarsening, which becomes stress concentration point during forming, becomes the starting point of crackle.Therefore, containing Si
When, Si contents are less than 0.20 mass %, are preferably suppressed to below 0.17 mass %.Also it is possible to be suppressed to 0 mass %.
(Mn：Less than 0.015 mass % (containing 0 mass %))
Mn is the element being mixed into as inevitable impurity, if Mn contents reach more than 0.015 mass %, crystal
(intermetallic compound) coarsening, which becomes stress concentration point during forming, becomes the starting point of crackle.Therefore, containing Mn
When, Mn contents are suppressed to less than 0.015 mass %.Furthermore it is preferred that being suppressed to less than 0.010 mass %, more preferably it is suppressed to low
In 0.005 mass %.Also it is possible to be suppressed to 0 mass %.
(Cr：(contain 0 mass %) below 0.015 mass %)
Cr is the element being mixed into as inevitable impurity, if Cr contents are higher than 0.015 mass %, crystal (gold
Compound between category) coarsening, which becomes stress concentration point during forming, becomes the starting point of crackle.When therefore, containing Cr,
Cr contents are suppressed to below 0.015 mass %.Also it is possible to be suppressed to 0 mass %.
(Ti：0.01～0.05 mass %)
For the miniaturization of ingot bar tissue, it is also possible to add Ti as Al-Ti-B intermediate alloys.I.e., it is also possible to will make
For Ti: the fine agent of Al-Ti-B ingot bars of B=5: 1 or 5: 0.2 ratio, liquation is added to the form of waffle ingot or foundry pig
In (put into slab solidification before smelting furnace, field trash filter, degasser, any one rank of liquid inventory control device
The liquation of section), with Ti gauge, it is allowed to containing by the end of 0.05 mass %.When Ti contents are less than 0.01 mass %, cannot get ingot bar
The effect of tissue miniaturization.On the other hand, if be higher than 0.05 mass %, crystal (intermetallic compound) coarsening, its into
Stress concentration point during to form, becomes the starting point of crackle.Therefore, when adding Ti, Ti contents are 0.01～0.05 matter
Amount %.
(surplus：Al and inevitable impurity)
Than that described above, surplus is made up of the composition of fin material Al and inevitable impurity.Further, as inevitable
Impurity, in addition to described Si, Mn, Cr, for example, in scope contained by parent metal, intermediate alloy, commonly known
Mg, Zn, Zr, Ce, Ga, V, Ni etc., are not less than in the range of 99.30 mass % in Al purity, respectively allow for containing by the end of
0.05 mass %.
(Al purity：More than 99.30 mass %)
When Al purity is less than 99.30 mass %, with the increase of intermetallic compound, aperture crackle increases, corrosion resistance
Reduce.Therefore, Al purity is more than 99.30 mass %.
(thickness of slab：Less than 0.115mm)
The present invention required according to the miniaturization of heat exchanger in recent years, lightweight and high performance etc., from realizing fin material
Thin-walled property from the viewpoint of, using thickness of slab less than 0.115mm fin material as object.Therefore, the thickness of slab of fin material is less than
0.115mm.In the present invention, the mean diameter of subgrain is limited in into less than 2.5 μm, even if being thin-walled, becomes rising for destruction
The possibility also very little of point, therefore, from feature this viewpoint that can further play the present invention, preferably shorter than
0.100mm, more preferably in below 0.090mm.
(the mean diameter of subgrain：Less than 2.5 μm)
It is anti-thread breakage less than the resistance to aperture of the fin material of 0.115mm in order to improve thickness of slab, need to make subgrain in alloy
Mean diameter is less than 2.5 μm.If the mean diameter of subgrain be higher than 2.5 μm, stress subgrain intragranular concentrate, crackle rise
Point increases, the anti-thread breakage reduction in resistance to aperture.Therefore, the mean diameter of subgrain is less than 2.5 μm.Further, lower limit is without special
Regulation, or 0 μm (i.e., it is also possible to without subgrain).By in such scope, even if because of solid solution Mn, solid solution Cu
Deng and occur processing hardening when, it is also possible to suppress the generation of aperture crackle, realize the raising of treatability.
Next, for the assay method of the mean diameter of subgrain is illustrated.
First, according to EBSD (Electron Back Scattered Diffraction Pattern) method, for from
Scanning electron microscope (SEM：Scanning Electron Microscopy) image crystalline structure carry out orientation point
Analysis.EBSD methods are to irradiate electron ray, the certain crystal orientations using the reflection electronic Kikuchi lines diffraction at this moment occurring to test portion
Method.In addition, in crystalline orientation analysis, such as TSL societies OIM (Orientation Imaging can be used
Microscopy, (registered trade mark)).
Also, the mean diameter of subgrain is the quantity that crystal grain is calculated according to the SEM/EBSD determination datas, uses fin material
The gross area divided by the quantity of crystal grain, the diameter when area of each crystal grain and approximate circle is defined as into the mean diameter of subgrain.
(yield strength：More than 130MPa and below 155MPa)
The fin material of the present invention is the fin material as combination (-type)press, so yield strength is more than 130MPa and 155MPa
Below., in below 130MPa, intensity is not enough for yield strength, and treatability during thin-walled property is reduced.On the other hand, if being more than
155MPa, then intensity is too high, and aperture crackle occurs when combination (-type)press shapes.Therefore, yield strength is more than 130MPa and 155MPa
Below.Further, preferably greater than 130MPa and below 150MPa, more preferably higher than 130MPa and below 140MPa.
The measure of yield strength, for example, can be carried out as follows：From on fin material, draw direction and rolling direction are made
Tension test sheet that is parallel and cutting No. JIS5, enforcement follow the tension test of JISZ2241.
Further, the mean diameter and yield strength of subgrain, can be by carrying out with manufacturing condition described later into being grouped into
Control.Specifically, the mean diameter of subgrain by the content of each composition, the heat treatment condition that homogenizes (temperature and time),
Hot finish to gauge end temp, cold working rate, quenched annealing conditions (temperature and time) etc. are controlled, and yield strength is contained by each composition
Amount, the heat treatment condition that homogenizes (temperature and time), quenched annealing conditions (temperature and time) etc. are controlled.
The fin material of the present invention can also possess surface treatment epithelium in wing sheet surface.Further, so-called wing sheet surface
Refer to the one or both sides of fin material.
(surface treatment epithelium)
As surface treatment epithelium, according to use environment and purposes, chemical conversion epithelium, resin involucra and inorganic skin can be enumerated
Film, it is also possible to be combined (resin involucra, inorganic epithelium are set on chemical conversion epithelium).In addition, as resin involucra, inorganic skin
Film, can enumerate corrosion-resistant resin epithelium, hydrophilic resin epithelium, hydrophilic inorganic epithelium, lubricity resin involucra etc., also may be used
So which is appropriately combined.
As chemical conversion epithelium, for example, can enumerate phosphoric acid chromate.As corrosion-resistant resin epithelium, can enumerate epoxy,
The resins such as polyurethane series, acrylic acid seriess, Polyester, its thickness are preferably 0.5～5 μm.As hydrophilic epithelium, water glass can be enumerated
The inorganic matters of glass system, containing resin as polyacrylic acid or polyacrylate, containing sulfonic group or sulfonic acid radical derivative so
Resin etc., its thickness is preferably 0.05～10 μm.As lubricity resin involucra, the resin containing polyether polyol can be enumerated
Deng preferably 0.1～10 μm of its thickness.
Make two among corrosion-resistant resin epithelium, hydrophilic resin epithelium, hydrophilic inorganic epithelium, lubricity resin involucra
When planting combination of the above, the face side preferably in corrosion-resistant resin epithelium arranges hydrophilic resin epithelium, in hydrophilic resin skin
Film, the face side of hydrophilic inorganic epithelium arrange lubricity resin involucra.
<The manufacture method of fin material>
The manufacture method of the fin material of the present invention is the manufacture method of above-mentioned fin material, carries out heat treatment step, Hot-roller
Sequence, cold working operation, quenched annealing operation.As needed, it is also possible to including ingot bar manufacturing process and surface treatment procedure.
Hereinafter, for each operation is illustrated.
(ingot bar manufacturing process)
Ingot bar manufacturing process be fusing, cast aluminium alloy gold and make the operation of aluminium alloy ingot bar.
In ingot bar manufacturing process, by the liquation for having melted the aluminium alloy with the chemical composition, regulation shape is made
Ingot bar.Fusing, the method for cast aluminium alloy gold are not particularly limited, using existing known method.For example, can be using true
Empty induction furnace fusing, is cast using continuous casting process, semi-continuous casting method.
(heat treatment step)
Heat treatment step is the aluminium alloy ingot bar for the chemical composition with the aluminium alloy, with 450～500 DEG C of temperature
Degree implements the operation of the heat treatment (homogenize heat treatment) of more than 1 hour.
When heat treatment temperature is less than 450 DEG C, homogenizing for the tissue of ingot bar is insufficient.In addition, causing the drop of hot-workability
It is low.In addition subgrain diameter becomes big.On the other hand, if being higher than 500 DEG C, in heating, between the fine metal of miniaturization, compound is thick
Bigization, subgrain coarsening and elongation percentage are reduced.Additionally, yield strength is uprised.In addition, causing the increase of solid solution capacity.Therefore, heat
Treatment temperature is 450～500 DEG C.In addition, if the heat treatment retention time is more than 1 hour, then the effect can be obtained, because
This does not need the special provision upper limit.On the other hand, if more than 10 hours, due to effect saturation, so in economy preferably
Heat treatment time is within 24 hours.
(hot-rolled process)
Hot-rolled process is that, after the heat treatment, the end temp with hot finish to gauge is 250 DEG C less than 300 DEG C of bar
Part implements the operation of hot rolling.
When the end temp of hot finish to gauge is less than 250 DEG C, the rolling of material is reduced, and rolling itself is difficult or strip thickness control becomes
Difficulty, productivity ratio are reduced.When on the other hand, more than 300 DEG C, because recrystallized structure is formed in hot rolled plate, quenched annealing
After generate fibrous identical crystalline orientation group, perforation ＆ produces constriction when rushing edge operation.In addition, subgrain diameter becomes big.Cause
This, the end temp of hot finish to gauge is 250 DEG C less than 300 DEG C.More preferably 260～290 DEG C.
(cold working operation)
Cold working operation is the operation of the cold working (cold rolling) for implementing cold working rate more than 96% after the hot rolling.
Hot rolling is carried out after terminating 1 time or repeatedly cold working, makes fin material become desired final thickness of slab.But, cold working
When rate is less than 96%, subgrain coarsening after quenched annealing.Therefore, cold worked cold working rate is more than 96%.Here, cold rnning
When carrying out intermediate annealing during work, cold working rate is the working modulus from after intermediate annealing to final thickness of slab.Therefore, if carrying out
Intermediate annealing, then reach more than 96% cold working rate difficulty, therefore do not carry out intermediate annealing.Further, because cold working rate is got over
It is high more preferred, so especially not setting the upper limit.
(quenched annealing operation)
Quenched annealing operation is, after the cold working, to implement to keep 1～6 hour quenched with 135～210 DEG C of temperature
The operation of annealing (final annealing).
When the temperature of quenched annealing is less than 135 DEG C, cannot get sufficient elongation percentage.On the other hand, if being higher than 210 DEG C,
Recrystal grain is produced after annealing, crackle occurs with which as starting point.In addition, the miniaturization of subgrain cannot promote.In addition
Treatability step-down.Therefore, the temperature of quenched annealing is 135～210 DEG C, and preferably 150 DEG C less than 180 DEG C.Further, adjust
Matter annealing is generally carried out more than 1 hour, the effect saturation if more than 6 hours, therefore the retention time is 1～6 hour.
(surface treatment procedure)
Surface treatment procedure is the operation for implementing surface treatment to the fin material after quenched annealing.
In surface treatment procedure, when forming chemical conversion epithelium, can be by using common application type or response type
The chemical conversion treatment of medicament is carrying out.Form the resins such as corrosion-resistant resin epithelium, hydrophilic resin epithelium, lubricity resin involucra
During epithelium, can be carried out by using the coating of roll coater, drying.
Further, when the present invention is carried out, each operation will not be being produced in the range of harmful effect, it is also possible in institute
State between each operation or in front and back including other operations.For example, it is also possible to remove the foreign body removal step of the foreign body such as waste, right
In ingot bar implement facing facing operation, after quenched annealing operation and surface treatment procedure, including appropriate reality
Apply the machining operation of machining etc. for making fin material needs.
Also, the fin material of so manufacture is formed by the manufacturing process based on compound mode processing.
Combination forming (combination (-type)press) is to implement to swell by the 1st operation, implements drawing and forming by the 2nd operation, by the 3rd operation
Implement punching and reaming processing (perforation ＆ rushes edge shaping), thinning drawing processing is implemented by the 4th operation, implements to expand again by the 5th operation
Mouth processing.Also, therefore resistance to aperture is anti-thread breakage excellent for the fin material of the present invention, it is possible to suppressing the shaping that compound mode is caused
The generation of aperture crackle during processing, can additionally improve treatability.
【Embodiment】
More than, for being set forth for the mode for implementing the present invention, below will confirm that the reality of the effect of the present invention
Apply example and contrasted with the comparative example of the important document for being unsatisfactory for the present invention, specifically illustrate.Further, the present invention is not implemented by this
The restriction of example.
(making for examination material)
(embodiment No.1～10, comparative example No.11～22)
Fusing, the aluminium alloy of composition shown in casting table 1 and make ingot bar, the ingot bar is implemented after facing, with 480
DEG C implement the heat treatment that homogenizes of 4 hours.For this through the ingot bar of heat treatment so that the end temp of hot finish to gauge is 270 DEG C
Mode is controlled and implements hot rolling, becomes the hot rolled plate of thickness of slab 3.0mm.Again respectively with 97.0% or 97.3% or so cold rnning
Work rate is implemented cold rolling and makes thickness of slab for after 90 μm and 80 μm, the quenched annealing of temperature and retention time shown in enforcement table 1 and make
Into fin material.
(embodiment No.23～28, comparative example No.29～36)
Aluminium alloy (with table 1 corresponding alloy A, B, C) shown in melting, casting table 2 and make ingot bar, the ingot bar is implemented
After facing, implement homogenize heat treatment, hot rolling, as the hot rolled plate of thickness of slab 3.0mm.Additionally, in addition to No.36, respectively
With 97.0% or 97.3% or so cold working rate implement it is cold rolling and after making thickness of slab as 90 μm and 80 μm, the quenched annealing of enforcement and make
Into fin material.No.36 be hot rolled plate for thickness of slab 3.0mm with 50% cold working rate implement it is cold rolling after, using batch furnace
Implement the intermediate annealing of 360 DEG C × 3 hours.Afterwards, then respectively implement cold rolling with 94.0% or 94.7% or so cold working rate,
Thickness of slab is made after 90 μm and 80 μm, to implement quenched annealing and fin material is made.Homogenize heat treatment, the end temp of hot finish to gauge,
The condition of quenched annealing is as shown in table 2.Further, No.31 can not manufacture fin material.
(embodiment No.37～40, comparative example No.41～44)
No.37 for the fin material same with the No.23 of table 2,38, the fin material same with the No.28 of table 2
No.39,40, the No.41 of the fin material same with the No.30 of table 2,42, the No.43 of the fin material same with the No.33 of table 2,
44, carry out following surface treatment (No.1～4).
No.1：Surface treatment with 1 the same terms of comparative example of Japanese Unexamined Patent Publication 2010-223520 publications (has in order
Standby chemical conversion epithelium, hydrophilic epithelium, lubricity epithelium)
No.2：Surface treatment with 1 the same terms of embodiment of No. 3383914 publications of Japanese Patent No. (possesses in order
Chemical conversion epithelium, hydrophilic epithelium, lubricity resin involucra)
No.3：Surface treatment with 1 the same terms of embodiment of Japanese Unexamined Patent Publication 2008-224204 publications (has in order
Standby chemical conversion epithelium, corrosion-resistant resin epithelium, hydrophilic epithelium)
No.4：Surface treatment with 21 the same terms of comparative example of Japanese Unexamined Patent Publication 2010-223514 publications (has in order
Standby chemical conversion epithelium, corrosion-resistant resin epithelium)
It is displayed in table 1 into being grouped into, manufacturing condition is displayed in table 2,3.Further, the scope of the present invention is unsatisfactory in table
Content, logarithm value draws underscore and represents, the composition not contained is represented with "-".Further, No.31 can not manufacture fin material, because
"-" is designated as in this one hurdle of quenched annealing.In addition, No.16 is (with document based on the aluminum alloy fin material described in patent documentation 1
The example 1 (but, the thickness of slab (3.5mm) after hot rolling end temp and hot rolling is different) of table 2, No.13 is based on patent documentation 2
Described aluminum alloy fin material (with the example 4 (but, processing mode (stretch process) is different) of the table 1 of document).In addition,
No.17 be based on described in patent documentation 3 aluminum alloy fin material (with the table 1 of document example 3 (but, processing mode is (non-
Stretch process) different)), No.35 is (with the example 11 of the table 2 of document based on the aluminum alloy fin material described in patent documentation 4
But (, it is cold rolling after thickness of slab (0.115mm is thick) it is different)).
Next, as the tissue morphology of fin material, determining the mean diameter of subgrain according to following method.Additionally,
Intensity and elongation percentage are determined by following method.
(mean diameter of subgrain)
The mean diameter of subgrain is calculated in accordance with the following methods, using scanning electron microscope (SEM), with 1,
000 times of observation multiplying power shoots test portion surface, for the crystalline structure of resulting image, with 0.10 μm of measuring interval, with logical
Based on crossing the data that EBSD methods have carried out orientation analysis, in TSL societies OIM (Orientation Imaging
Microscopy, (registered trade mark)) calculated on software automatically.That is, number is determined divided by by SEM/EBSD with the gross area of fin material
The quantity of crystal grain according to statistics, makes the area of each crystal grain approximate with circle, diameter at this moment is defined as the mean diameter of subgrain.
Further, the quantity of crystal grain is that to will abut against the crystal grain surrounded by crystal grain boundary of the intercrystalline misorientation within 2 ° brilliant as one
Grain is being counted.
(tensile strength, 0.2% yield strength, elongation percentage)
From on fin material, make draw direction parallel with rolling direction and cut the tension test sheet of No. JIS5.Tested with this
Piece, implements the tension test based on JISZ2241, determines tensile strength, 0.2% yield strength and elongation percentage.Further, this enforcement
Carried out with the draw speed of 5mm/min in the evaluation of example and comparative example.
(resistance to aperture anti-thread breakage evaluation)
Fin material to making implements extrusion molding by combination forming, evaluates resistance to aperture anti-thread breakage.
The anti-thread breakage evaluation in resistance to aperture be the crackle produced in orifice part by 400 holes range estimations for extrusion molded article simultaneously
Counted to be evaluated.
Using " crackle number/400 × 100 (%) " as incidence rate, it is (zero) that more than 10% is (×) less than 10%.Then,
90 μm and 80 μm is entirely (zero) for qualified.
(treatability evaluation)
Fig. 1 is for illustrating (a) axonometric chart of the evaluation methodology of treatability and (b) side view.The aperture of 10 will be provided with
Fin material 1 (200mm length × 20mm width) with the multiple stackings of 1.6mm spacing, lead to 10 copper pipes 2 of external diameter 7mm, internal diameter 6mm
Each aperture is crossed, and buret is inserted in the inner side of copper pipe 2 and is carried out expander, be thus fixed, makes heat exchanger.
Rustless steel clamp dog 3 of the bottom surface for 20mm square is arranged on force cell, the side of heat exchanger is placed in,
Apply compressive load, determine the load that fin material 1 starts flexing.
Start the load of flexing in more than 4500N, be judged to that treatability is good (zero), during less than 4500N, be judged to place
Rationality bad (×).
Measurement result and evaluation result are displayed in table 1～3.Further, the content of the scope of the present invention is unsatisfactory in table, it is right
Numerical value draws underscore and represents, the manufacture due to carrying out fin material, therefore can not be measured and evaluate, and is represented with "-".
【Table 1】
【Table 2】
【Table 3】
(evaluation based on composition)
As shown in table 1, as No.1～10 of embodiment, because meeting the scope of the present invention, resistance to aperture is anti-thread breakage
It is excellent with treatability.
On the other hand, as No.11～22 of comparative example, because being unsatisfactory for the scope of the present invention, for following knot
Really.
Because Si contents are higher than higher limit, thick intermetallic compound increases No.11, the anti-thread breakage difference in resistance to aperture.
Because Fe contents are less than lower limit, subgrain diameter becomes big to No.12, and resistance to aperture is anti-thread breakage and treatability is poor.
No.13 is because Fe contents are higher than higher limit, in addition, Al purity is less than lower limit, so thick intermetallic compound increases, and it is resistance to
The anti-thread breakage difference in aperture.Because Al purity is less than lower limit, thick intermetallic compound increases No.14, the crackle of resistance to aperture
Property is poor.
No.15 causes processing hardening, the anti-thread breakage difference in resistance to aperture because Cu contents are higher than higher limit.No.16 is because Mn
Content is higher than higher limit, so thick intermetallic compound increases, the anti-thread breakage difference in resistance to aperture.No.17 and No.18 is because Mn contains
Amount is higher than higher limit, so thick intermetallic compound increases, in addition, the temperature of quenched annealing is higher than higher limit, and so sub-
Crystal grain diameter becomes big, and yield strength is less than lower limit in addition, and resistance to aperture is anti-thread breakage and treatability is poor.
Because Cr contents are higher than higher limit, thick intermetallic compound increases No.19, the anti-thread breakage difference in resistance to aperture.
Because Ti contents are higher than higher limit, thick intermetallic compound increases No.20, the anti-thread breakage difference in resistance to aperture.No.21 because
Ti contents are higher than higher limit, so thick intermetallic compound increases, because the temperature of quenched annealing is higher than higher limit,
Resistance to aperture is anti-thread breakage and treatability is poor.Because Fe contents are higher than higher limit, thick intermetallic compound increases No.22,
The anti-thread breakage difference in resistance to aperture.
(evaluation based on manufacture method)
As shown in table 2, as No.23～28 of embodiment, because meeting the scope of the present invention, resistance to aperture is anti-thread breakage
It is excellent with treatability.
On the other hand, as No.29～36 of comparative example, because being unsatisfactory for the scope of the present invention, become following
As a result.
Because the temperature of the heat treatment that homogenizes is less than lower limit, subgrain diameter becomes big to No.29, and yield strength is low,
Treatability is poor.Because the temperature of the heat treatment that homogenizes is higher than higher limit, subgrain becomes big to No.30, the anti-thread breakage difference in resistance to aperture.
, because the end temp of hot finish to gauge is less than lower limit, rolling itself is difficult, it is impossible to carry out fin material for No.31
Manufacture.Because the end temp of hot finish to gauge is higher than higher limit, subgrain becomes big to No.32, and yield strength is low, the crackle of resistance to aperture
Property and treatability are poor.No.33 becomes mixed grain structure, in addition, yield strength is less than down because refining temperature is higher than higher limit
Limit value, resistance to aperture is anti-thread breakage and treatability is poor.
Because refining temperature is less than lower limit, yield strength is higher than higher limit to No.34, is split in the operation that swells
Stricture of vagina.Because the temperature of the heat treatment that homogenizes is higher than higher limit, subgrain becomes big to No.35, the anti-thread breakage difference in resistance to aperture.No.36
Because having carried out intermediate annealing, cold working rate is less than lower limit.Therefore, the mean diameter of subgrain is higher than higher limit, separately
Outward, yield strength is less than lower limit, and resistance to aperture is anti-thread breakage and treatability is poor.
(implementing evaluation during surface treatment)
The resistance to aperture of the fin material for implementing surface treatment of No.37～44 is anti-thread breakage, with do not implement be surface-treated
Fin material is same result.
Further, the fin material of No.16,13,17,35, be envisioned for respectively patent documentation 1, patent documentation 2, patent documentation 3,
Existing aluminum alloy fin material described in patent documentation 4.As shown in this embodiment, these existing aluminum alloy fin materials are described
Evaluation in be unsatisfactory for certain level.Therefore, according to the present embodiment, the combination (-type)press heat exchanger aluminium alloy of the present invention
The fact that fin material is more excellent than existing aluminum alloy fin material is objective clear.
More than, for the fin material and its manufacture method of the present invention, show that embodiment and embodiment have been carried out specifically
It is bright, but the purport of the present invention do not limited by the content.Further, present disclosure certainly also can based on it is above-mentioned describe into
The extensive change of row, change etc..
1 fin material
2 steel pipes
3 pieces
Claims (5)
1. a kind of heat exchanger aluminum alloy fin material, it is characterised in that be made up of aluminium alloy, the aluminium alloy contains Fe：
0.010～0.4 mass %, Cu：0.005～0.05 mass %, surplus are made up of Al and inevitable impurity, and Al purity is
More than 99.30 mass %, the thickness of slab of the heat exchanger aluminum alloy fin material is less than 0.115mm, the mean diameter of subgrain
For less than 2.5 μm, and yield strength is higher than 130MPa and below 155MPa, and which is by the shaping based on combination (-type)press mode
Method and the processing that is formed.
2. heat exchanger aluminum alloy fin material according to claim 1, it is characterised in that in the chemistry of the aluminium alloy
In composition, Si is suppressed to：Less than 0.20 mass %, Mn：Less than 0.015 mass %, Cr：Below 0.015 mass %.
3. the heat exchanger aluminum alloy fin material according to claim 1 or claim 2, it is characterised in that described
In the chemical composition of aluminium alloy, also contain Ti：0.01～0.05 mass %.
4. the heat exchanger aluminum alloy fin material according to claim 1 or claim 2, it is characterised in that in fin
Material surface possesses surface treatment epithelium.
5. a kind of manufacture method of heat exchanger aluminum alloy fin material, is the heat exchange described in claim 1 or claim 2
The manufacture method of device aluminum alloy fin material, it is characterised in that carry out following operation：
For the aluminium alloy ingot bar of the chemical composition with the aluminium alloy, implemented more than 1 hour with 450～500 DEG C of temperature
Heat treatment heat treatment step；
After the heat treatment, the end temp with hot finish to gauge is 250 DEG C of heat less than 300 DEG C of condition enforcement hot rolling
Roll operation；
After the hot rolling, implement the cold worked cold working operation of cold working rate more than 96%；
After the cold working, implement the quenched annealing operation of quenched annealing, the quenched annealing is with 135～210 DEG C of temperature
Degree keeps the process of 1～6 hour,
By the forming operation of the manufacturing process based on combination (-type)press mode.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2012221659A JP5830451B2 (en) | 2012-10-03 | 2012-10-03 | Aluminum alloy fin material for heat exchanger for combination press |
| JP2012-221659 | 2012-10-03 | ||
| PCT/JP2013/075890 WO2014054485A1 (en) | 2012-10-03 | 2013-09-25 | Combination-pressable aluminum-alloy fin material for heat exchanger and method for producing same |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN104685082A CN104685082A (en) | 2015-06-03 |
| CN104685082B true CN104685082B (en) | 2017-04-05 |
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| CN201380051304.4A Expired - Fee Related CN104685082B (en) | 2012-10-03 | 2013-09-25 | Combination (-type)press heat exchanger aluminum alloy fin material and its manufacture method |
Country Status (3)
| Country | Link |
|---|---|
| JP (1) | JP5830451B2 (en) |
| CN (1) | CN104685082B (en) |
| WO (1) | WO2014054485A1 (en) |
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| JP2014224323A (en) * | 2014-07-01 | 2014-12-04 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger and heat exchanger |
| JP2014231641A (en) * | 2014-07-01 | 2014-12-11 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger of combination press |
| JP7337939B2 (en) * | 2019-09-03 | 2023-09-04 | 日本軽金属株式会社 | Luminous aluminum alloys and lustrous aluminum alloy die-cast materials |
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| Publication number | Priority date | Publication date | Assignee | Title |
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| JPH08313191A (en) * | 1995-03-16 | 1996-11-29 | Furukawa Electric Co Ltd:The | Aluminum fin material for heat exchanger |
| JP4053793B2 (en) * | 2002-03-08 | 2008-02-27 | 古河スカイ株式会社 | Manufacturing method of aluminum alloy composite for heat exchanger and aluminum alloy composite |
| JP4856368B2 (en) * | 2004-09-08 | 2012-01-18 | 株式会社神戸製鋼所 | Aluminum alloy fin material with excellent formability |
| CN100500904C (en) * | 2007-08-03 | 2009-06-17 | 乳源东阳光精箔有限公司 | Aluminum foil used for heat exchanger and manufacturing method thereof |
| JP2009250510A (en) * | 2008-04-04 | 2009-10-29 | Mitsubishi Electric Corp | Heat exchanger and its manufacturing method |
| JP5060632B2 (en) * | 2010-09-03 | 2012-10-31 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger and manufacturing method thereof |
| MY161707A (en) * | 2011-03-31 | 2017-05-15 | Kobe Steel Ltd | Drawless-press heat-exchanging aluminium alloy fin material and manufacturing method for the same |
| JP5693333B2 (en) * | 2011-03-31 | 2015-04-01 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger for combination press |
| JP5828657B2 (en) * | 2011-03-31 | 2015-12-09 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger |
| JP5843462B2 (en) * | 2011-03-31 | 2016-01-13 | 株式会社神戸製鋼所 | Aluminum alloy fin material for heat exchanger for drawless press |
-
2012
- 2012-10-03 JP JP2012221659A patent/JP5830451B2/en not_active Expired - Fee Related
-
2013
- 2013-09-25 CN CN201380051304.4A patent/CN104685082B/en not_active Expired - Fee Related
- 2013-09-25 WO PCT/JP2013/075890 patent/WO2014054485A1/en active Application Filing
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| Publication number | Publication date |
|---|---|
| CN104685082A (en) | 2015-06-03 |
| WO2014054485A1 (en) | 2014-04-10 |
| JP2014074199A (en) | 2014-04-24 |
| JP5830451B2 (en) | 2015-12-09 |
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