KR101216246B1 - Process for producing an aluminium alloy brazing sheet aluminium alloy brazing sheet - Google Patents

Abstract

The present invention relates to a method for producing an aluminum alloy brazing sheet, the method of producing an Al-Mn alloy sheet having an improved liquid film transition resistance when used as a core alloy in a brazing sheet, wherein the steps include: Casting a composition having: 0.5 <Mn <1.7, 0.06 <Cu <1.5, Si <1.3, Mg <0.25, Ti <0.2, Zn <2.0, Fe <0.5, 0.05 <Zr <0.25 and 0.05 <Cr <0.25 One or more elements selected from the group consisting of: <0.05, other elements in total <2.0, balance aluminum; Homogenization and preheating step; Hot rolling step; Cold rolling step (including intermediate annealing if necessary), the homogenization temperature is maintained for more than 1 hour at 450 ℃ or more, then air-cooled at a rate of 20 ℃ / h or more, the preheating temperature is 0.5 hours at 400 ℃ or more It is characterized in that it is maintained during the above.

Description

Manufacturing method of aluminum alloy brazing sheet and aluminum alloy brazing sheet {PROCESS FOR PRODUCING AN ALUMINIUM ALLOY BRAZING SHEET, ALUMINIUM ALLOY BRAZING SHEET}

The present invention relates to a method for producing an Al-Mn alloy sheet having improved liquid film migration resistance when used as a core alloy in a brazing sheet material. In addition, the present invention relates to an Al-Mn alloy sheet prepared according to the production method and the use of the sheet.

In brazing applications, a phenomenon known as "liquid film migration" or liquid film migration (LFM), degrades the overall performance of brazing products such as evaporators, radiators, heater cores and the like. In the literature, the term "LFM" is also referred to as "core dissolution" or "core penetration" or "core erosion". The term "LFM" is used herein to refer to both of these terms. The exact mechanism that causes the LFM is not yet fully understood, but the severity of the LFM seems to be augmented by the presence of a certain amount of dislocation in the core alloy of the brazing sheet. The sensitivity of the material to LFM is comparable to the soft and slightly cold worked conditions of the same material, such as complete annealing (O-tempering) and stress hardening and / or stress relaxation tempering (eg H14, H24, etc.). Relatively low. The term “slight cold working” typically refers to variations resulting from industrial processes such as stamping, roll forming, or tensile leveling that are applied to manufacture components of heat exchangers such as evaporators or oil cooler core plates, folded tubes, etc. deformation). The brazing sheet composed of the core alloy and the Al-Si clad alloy is deformed to form the product, and when subsequent brazing cycles are performed, a small amount of deformation appears to be sufficient to induce LFM in the brazing sheet. As the LFM proceeds deep into the core alloy, the brazing, strength and corrosion resistance deteriorate. Alloying elements that retard recrystallization, such as chromium, zirconium and vanadium, are known to enhance susceptibility to LFM. Manganese dispersoids are also known to delay recrystallization and thus enhance susceptibility to LFM. The amount and size of manganese desopheroid depends on the processing path of the brazing sheet.

For brazing applications, the core alloy of the brazing sheet product requires a good combination of strength and formability. Clearly, the sensitivity to LFM should be at a level low enough to ensure adequate corrosion and braking. High strength can be obtained by alloying with an element such as silicon, manganese, chromium, zirconium or vanadium. However, these alloying elements also increase the susceptibility to LFM. The use of non O-tempers, such as H14-temper or H24-temper, has also been proposed to reduce sensitivity to LFM. However, these tempers effectively reduce the LFM, but often impair the moldability of the brazing sheet product. Other optional processes, such as light cold deforming processes such as tensile leveling, or the use of non-recrystallized surface layers, are difficult to control in mass production runs and may therefore impair reproducibility and / or formability.

It is an object of the present invention to provide an Al-Mn alloy sheet having an improved liquid film transition resistance when used as a core alloy in a brazing sheet, wherein a good strength / formulation combination of the alloy has a sufficiently low sensitivity to LFM and adequate resistance. Combined with corrosiveness.

It is also an object of the present invention to provide a method for producing the Al-Mn alloy sheet in which an easily controllable and reproducible product is obtained.

It is also an object of the present invention to provide a method for producing an Al-Mn alloy sheet having improved liquid film transition resistance in a stripped tube, evaporator or oil cooler core plate, finstock, wherein the alloy has good strength / molding. The combination of properties is combined with sufficiently low sensitivity to LFM, adequate brazing and corrosion resistance.

According to the present invention, the at least one object consists of a method for producing an Al-Mn alloy sheet having improved liquid film transition resistance when the aluminum alloy sheet is used as a core alloy in a brazing sheet, the method comprising

Casting a composition having the following composition (% by weight):

  0.5 <Mn <1.7, preferably 0.6-1.7

  0.06 <Cu ≤ 1.5, preferably 0.2-1.5

  0 <Si <1.3, preferably 0 <Si <0.8, more preferably 0 <Si <0.3

  ㅇ 0 <Mg ≤ 0.25

  ㅇ 0 <Ti <0.2

  ㅇ 0 <Zn ≤ 2.0

  ㅇ 0 <Fe ≤ 0.5

  0 <Zr <0.05 and 0.05 <Cr <0.25

  ㅇ Other elements, balance aluminum of <0.05, total <0.20, respectively

Homogenization and preheating step;

ㆍ Hot Rolling Step

Cold rolling step (including intermediate annealing if necessary),

The homogenization temperature is maintained at 450 ℃ or more for 1 hour or more, followed by air cooling at a rate of 20 ℃ h or more,

The preheating temperature is maintained for at least 400 hours at 400 ℃ or more.

Casting is accomplished using regular production techniques such as DC casting or continuous casting.

The process according to the invention enables the production of Al-Mn alloys when used as core alloys in brazing sheets, in which a good strength / forming combination is combined with significantly lower sensitivity to LFM and sufficient corrosion resistance. The present inventors have reported that chromium has an adverse effect on the sensitivity to LFM due to the delay effect on the recrystallization of the alloy, but the combination of the alloy's chemical properties and process parameters, in particular homogenization and preheating, has a sufficiently low sensitivity to LFM. The results found the surprising fact that a product with sufficient internal stone was obtained. Cr-containing and / or Zr-containing precipitates formed in the alloy as a result of the combination of composition and treatment conditions reduce the susceptibility to LFM. In addition, chromium enhances the strength of the alloy while recrystallization of the alloy achieves sufficient formability. The inventors have found that similar results can be obtained by alloying with V or alloying V with Cr and / or Zr.

In an embodiment of the invention, the Cr and / or Zr content is at least 0.08% by weight. We have found that a combination of chromium content of at least 0.08% by weight or zirconium content of at least 0.08%, or combinations thereof in combination with the aforementioned treatment conditions, results in high strength combined with sufficient LFM-resistance.

In an embodiment of the invention, the maximum magnesium content is at least 0.1% by weight, preferably at least 0.05% by weight. The magnesium content should be as low as possible to avoid the deleterious effects of magnesium on the flux used during controlled atmosphere brazing. In an embodiment of the invention, the copper content is from 0.7 to 1.2% by weight.

In an embodiment of the present invention, the manganese content is 0.7 to 1.4 wt%. If the manganese content exceeds 1.4% by weight, the manufacturability is worsened, the alloy strength is less than 0.7% by weight. In embodiments of the invention, the maximum zinc content is preferably 0.4% by weight to prevent excessive anodization of the core alloy in certain applications. In an embodiment of the present invention, the iron content is preferably 0.35% by weight or less to prevent the formation of undesirable large iron containing intermetallics during industrial scale casting runs.

In an embodiment of the invention, the homogenization temperature is between about 530 ° C. and 620 ° C., preferably between 530 ° C. and 595 ° C., preferably maintained for 1 to 25 hours, more preferably 10 to 16 hours, and preheated. The temperature is between about 400 ° C. and 530 ° C., preferably between 420 ° C. and 510 ° C., preferably between 1 and 25 hours, more preferably between 1 and 10 hours. In the alloy according to the invention, an optimum compromise between strength, formability, susceptibility to LFM and corrosion resistance was found when homogenization temperature and time and preheat temperature and time were chosen within a given boundary, an especially interesting compromise being the alloy Was obtained upon treatment in accordance with the preferred temperatures and times described above.

It is known to those skilled in the art that the present invention usually does not independently select annealing time and temperature. The most relevant metallurgical treatment is thermally active and is obtained in situations where high temperatures combined with short time can yield the same results as low temperature and long time.

The process according to the invention also comprises the step of recrystallization annealing at a sufficient annealing temperature-annealing time combination after cold rolling to promote substantially complete recrystallization of the Al-Mn alloy. Under these conditions, the highest moldability is obtained.

In an embodiment of the present invention, the maximum silicon content of the Al-Mn alloy is 0.3% by weight. In a preferred embodiment of the present invention, the maximum silicon content of the Al-Mn alloy is 0.15% by weight. Silicon is known to increase susceptibility to LFM. Therefore, the silicon content should be selected as low as possible. However, the inventors have found that when using a silicon content of up to 0.3% by weight, preferably up to 0.15% by weight, a sufficient combination of sensitivity and strength to LFM is obtained.

In an embodiment of the invention, Cr≤0.18% by weight, preferably at least 0.06% by weight, more preferably 0.08% by weight <Cr≤0.15% by weight, most preferably 0.08% by weight <Cr≤0.12% by weight. . When the Cr value exceeds 0.18% by weight, casting of Al-Mn alloy becomes very difficult due to the formation of large intermetallic compounds. Al-Mn alloys having a Cr content of 0.15 wt% or less or 0.12 wt% or less have no problem in casting. By adding 0.08% by weight or more of Cr, in combination with the treatment conditions described above, a susceptible effect of chromium on LFM is obtained with a sufficient combination of sensitivity and strength to LFM. Precipitates formed in the alloy as a result of the combination of composition and treatment conditions reduce the susceptibility to LFM. In an embodiment of the invention, the process also includes cladding at least one side of the Al—Mn alloy with an AA4000 series or Al—Si brazing alloy optionally comprising up to 2.0 wt.% Zn. Cladding may be performed by any other known technique such as roll bonding or spray cladding or cast cladding.

In addition, the present invention can be implemented as a sheet product prepared according to the method as described above, the elongation before brazing is at least 18%, preferably at least 19%, more preferably at least 21% and / or at least 0.270 brazing It has a total n-value and / or tensile strength after brazing of at least 140 MPa, preferably at least 150 MPa. Elongation was measured through a gauge length of 80 mm (denoted A80).

In an embodiment of the present invention, the coupon SWAAT validity after brazing cut specimen measured in days condition that perforation occurs in the test according to ASTM G85 A3 is not less than 15 days, preferably 2O Is more than a day. Low susceptibility to LFM is reflected in improved corrosion resistance in heat exchanger components after brazing.

In an embodiment of the invention, the sheet described above comprises 0.5-5.0% by weight, preferably 0.5, of a non-brazing liner or waterside liner alloy or Zn such as AA7072, AA1145 or AA3005. It is applied as a folded tube in brazing sheets with or without Al-Mn-based alloys containing 2.5% by weight or as a core used under similar conditions. Requirements for strength, formability, LFM susceptibility and corrosion resistance relate particularly to the application of the sheet as a core in a brazing sheet for application in heat exchangers using folded tubes, for example.

Sheet materials produced according to the invention described above can be used in the manufacture of components of tube-finned heat exchangers such as radiators, heater cores and condensers, or plate-finned heat exchangers such as evaporators or oil cooler core plates or radiator tanks or heater cores. It is particularly useful as a core alloy in a brazing sheet for producing a component of a core or in a brazing fin stock material for producing a component for a heat exchanger.

Particular embodiments of the invention will be illustrated through the following non-limiting examples.

These alloys (alloys 1-4) were homogenized at various temperatures for various times. These alloys were then clad on both sides with 10% thickness AA4045, preheated for various hours at various temperatures prior to hot rolling, and hot annealed at 6.5 mm and then inter annealed at 350 ° C. for 3 hours. The first cold rolled to 2.3 mm, followed by intermediate annealing for 3 h at 350 ° C. and a second cold rolled to a final gauge of 0.5 mm. These alloys were recrystallized annealed to promote substantial complete recrystallization. To test the LFM behavior, the material was drawn between 2 and 10%. The drawing level showing the deepest penetration was used for the LFM data in Table 2.

Alloys 5 and 6 were each clad on both sides with 10% thickness AA4045, preheated prior to hot rolling, then hot rolled to 3.5 mm and cold rolled to 0.41 mm without intermediate annealing. After cold rolling, the material was recrystallized annealed to promote substantial complete recrystallization. LFM behavior was tested as described above. The results are shown in Table 2. Alloys designated as 'standard' are those used in LFM-critical applications.

In Table 2:

"+/-" means penetration between 50 and 60% of the core alloy thickness.

"+" Means penetration between 30 and 50% of the core alloy thickness.

"++" means <30% penetration of the core alloy thickness.

Since elongation usually exhibits a large scatter, the n-value can be used as an optional indicator of formability. An n-value of 0.270 or higher indicates good formability in view of the minimum required strength of 140 MPa or higher. Compared to standard alloys for LFM-critical applications, alloys according to the invention, such as alloys 2-6, provide equivalent LFM performance as shown in Table 2 and provide significantly higher post-brazing tensile properties.

Other specific alloys that can be prepared using the process according to the invention have the following composition (% by weight) ranges.

Si 0.8-1.0, and typically about 0.9

Fe 0.25-0.4, and typically about 0.35

Cu 0.25-0.45, and typically about 0.40

Mn 0.55-0.9, and typically about 0.85

Mg 0.1-0.22, and typically about 0.15

Zn 0.06-0.10, and typically about 0.08

Cr 0.06-0.10, and typically about 0.08

Zr 0.06-0.10, and typically about 0.08

Balance aluminum and unavoidable impurities

This alloy can be used in particular for tube plates, side supports and header tanks.

The present invention is not limited to the above-described embodiment, and various changes can be made without departing from the technical spirit of the claims.

Claims (16)

A method for producing Al-Mn alloy sheet having improved liquid film transition resistance when used as a core alloy in a brazing sheet, The manufacturing method Casting a composition having the following composition (% by weight):   ㅇ 0.5 <Mn ≤ 1.7   ㅇ 0.06 <Cu ≤ 1.5   ㅇ 0 <Si ≤ 0.15   ㅇ 0 <Mg ≤ 0.25   ㅇ 0 <Ti <0.2   ㅇ 0 <Zn ≤ 2.0   ㅇ 0 <Fe ≤ 0.5   0.05 <Cr <0.25 and 0 <Zr <0.05   ㅇ Other elements, balance aluminum of <0.05, total <0.20, respectively Homogenization and preheating step; Hot rolling step; Cold rolling with or without intermediate annealing, The homogenization temperature is maintained at 450 ℃ or more for 1 hour or more, followed by air cooling at a rate of 20 ℃ / h or more, The preheating temperature is Al-Mn alloy sheet manufacturing method characterized in that it is maintained for more than 0.5 hours at 400 ℃ or more. The method of claim 1, The homogenization temperature is maintained for 1 to 25 hours at 530 ℃ to 620 ℃, The preheating temperature is Al-Mn alloy sheet manufacturing method characterized in that maintained for 1 to 25 hours at 400 ℃ to 530 ℃. 3. The method according to claim 1 or 2, Mn is an Al-Mn alloy sheet manufacturing method, characterized in that 0.7 to 1.4% by weight. 3. The method according to claim 1 or 2, A method of producing Al-Mn alloy sheet, characterized in that Cr ≤ 0.18% by weight. 3. The method according to claim 1 or 2, Al-Mn alloy sheet manufacturing method characterized in that Mg ≤ 0.15% by weight. 3. The method according to claim 1 or 2, Al-Mn alloy sheet manufacturing method characterized in that Zn ≤ 0.4% by weight. 3. The method according to claim 1 or 2, And cladding at least one surface of the Al-Mn alloy with an Al-Si brazing alloy comprising at most 2.0 wt.% Zn as an optional element. 3. The method according to claim 1 or 2, Al-Si brazing alloys having a non-brazing liner alloy selected from the group consisting of AA7072, AA1145, AA3005, or Al-Mn-based alloys containing up to 2.0 wt% Zn as an optional element and containing 0.5-5.0 wt% Zn Al-Mn alloy sheet manufacturing method characterized in that it further comprises the step of cladding at least one surface of the Al-Mn alloy. A sheet made according to claim 1 or 2, wherein the elongation before brazing is at least 18%. The method of claim 9, A sheet characterized by a tensile strength of at least 140 MPa after brazing. The method of claim 9, A sheet characterized by an n-value of at least 0.270 before brazing. The method of claim 9, Post-brazing cut specimens tested in accordance with ASTM G85 A3, characterized in that the SWAAT life is more than 15 days without puncture. A sheet made according to claim 1, comprising combining a sheet as core alloy with a clad to form a brazing sheet for the manufacture of components of a tube-finned heat exchanger selected from the group consisting of a radiator, a heater core and a condenser. How to use. 1. The method of claim 1, comprising combining the sheet as a core alloy with a clad to form a brazing sheet for the manufacture of components of a plate-fin heat exchanger selected from the group consisting of evaporator or oil cooler core plates or radiator tanks or heater cores. Method of use of the sheet prepared according to paragraph 2. A method of using a sheet made according to claim 1 or 2 comprising combining a sheet as core alloy with a clad to form a brazing sheet for producing a component of a heat exchanger. delete