JP3274177B2 - Copper base alloy for heat exchanger and method for producing the same - Google Patents

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a suitable and highly reliable copper base alloy for heat exchangers used as a constituent material of various industrial and domestic heat exchangers such as radiators for automobiles and a method for producing the same.

[0002]

2. Description of the Related Art Conventionally, copper-based alloys have been used for radiators for automobiles, heat exchangers for various industries or homes, and the like. In the case of radiators for automobiles, they are mainly used as materials for tanks, plates, tubes and fins constituting the radiators. Particularly, tanks, plates and tubes are excellent in strength and formability such as brass 1 type or brass 2 types. Soft copper-based alloys have been used.

[0003] In recent years, there has been a strong demand for weight reduction of automobiles and high reliability of materials, and individual parts of automobiles have been reduced in weight and high in reliability.
However, brass materials such as brass type 1 or brass type 2 used in the above-described automotive radiator may cause dezincification corrosion or stress corrosion cracking, and thus have a problem in reliability. Was. In addition, for weight reduction, there has been a strong demand for further improvement in strength after satisfying required molding workability.

[0004] Dezincification corrosion and stress corrosion cracking occurring in a radiator for an automobile using a brass material as a member are considered to be due to the following reasons. Usually, the radiator is forcibly cooled by air, so SO ₂ in the air,
Such as the corroded NO _x and Cl ₂ gas. In addition, an environment that is susceptible to corrosion is created by the addition of snowmelt (NaCl or the like) or the addition of moisture into the engine room. Furthermore, a cooling medium is refluxed inside the radiator, and when used for a long period of time, corrosion products and dirt are generated. The life of the radiator has been shortened because dezincification corrosion, intergranular corrosion, pitting corrosion, etc. occur from the inside due to impact corrosion or the like.

[0005] Further, the long life coolant liquid (LLC) in the radiator has a low replacement frequency due to a decrease in the concentration of a rust inhibitor contained in the liquid and corrosion due to eluted metal ions. Needed to be higher. Furthermore, in each part of the radiator, residual stress due to molding and stress such as caulking at the time of assembly may cause stress corrosion cracking in combination with a corrosive environment, causing serious defects such as liquid leakage.

[0006]

SUMMARY OF THE INVENTION The present invention solves the above-mentioned problems of the prior art and is excellent in corrosion resistance such as stress corrosion cracking resistance, and excellent in strength, proof stress, molding workability and solderability. It is an object of the present invention to provide an inexpensive copper base alloy for a heat exchanger and a method for producing the same.

[0007]

Means for Solving the Problems The inventors of the present invention have conducted intensive studies to solve the above-mentioned problems.
By adding an appropriate amount at a regulated rate, and further adding an appropriate amount of B, the corrosion resistance of brass, especially the stress corrosion cracking resistance, can be significantly improved, and at the same time, the properties such as strength, proof stress, and formability can be improved. It was found that the present invention was achieved.

That is, the present invention firstly provides Zn: 8 to 25%, Ni: 0.1 to 1.5%, and Sn: 0.1% by weight.
1 to 1.2%, P: 0.001 to 0.10%, B: 0.001 to 0.06%
And the sum of the above-mentioned weight percents of Ni and Sn is 0.4 to 2.5 weight percent, and the ratio of the weight percentage of Ni / P is in the range of 5 to 50, with the balance being Cu and unavoidable impurities. An object of the present invention is to provide a copper base alloy for a heat exchanger, wherein a Ni-P-based compound is uniformly dispersed.

[0009] The copper base alloy for a heat exchanger can be obtained as an alloy having a crystal grain size of 0.005 to 0.030 mm. When this condition is satisfied, the copper base alloy for a heat exchanger is more preferable. . In addition, the tensile strength is 35kg
It can be obtained as an alloy of f / mm ² or more. Furthermore, it is possible to obtain an alloy having an Erichsen value of 10 mm or more.

[0010] The present invention secondly discloses that, in weight percent, Z
n: 8 to 25%, Ni: 0.1 to 1.5%, Sn: 0.1 to 1.2
%, P: 0.001 to 0.10%, B: 0.001 to 0.06%,
And the sum of the weight percent of Ni and the weight percent of Sn is 0.4 to
2.5% by weight, and the ratio of the weight percentage of Ni / P is 5 to
The alloy material consisting of Cu and inevitable impurities is cold-rolled at a reduction rate of 20 to 70%, and then recrystallized. After the final annealing of the recrystallization, 1 to 15 %
Cold-rolled at a sheet thickness reduction rate of 5 to 100 to 400 ° C.
An object of the present invention is to provide a method for producing a copper-based alloy for a heat exchanger, wherein low-temperature annealing is performed for 600 seconds.

[0011]

The reasons for limiting the alloy components of the present invention and the effects thereof will be described below.

[0012] Zn has the effect of improving the strength, moldability and heat resistance of the soldered portion. These effects are not sufficient when the Zn content is less than 8% by weight, %, It tends to cause dezincification corrosion and stress corrosion cracking even in the presence of Ni, Sn, and P. (In addition, Zn content in the presence of Ni, Sn, and P
If it exceeds 25%, side cracks tend to occur during hot rolling. Therefore, the content of Zn in the present invention is 8 to 25.
% By weight.

Ni has the effect of improving the strength, proof stress, heat resistance and stress corrosion cracking resistance. These effects are insufficient when the Ni content is less than 0.1% by weight, If it exceeds 300, workability will deteriorate.
Therefore, the content of Ni in the present invention is in the range of 0.1 to 1.5% by weight.

Sn has the effect of improving the strength, dezincification corrosion resistance and stress corrosion cracking resistance, and these effects are not sufficient if the Sn content is less than 0.1% by weight. %, The hot workability deteriorates. Therefore, the content of Sn in the present invention is 0.1 to
It was in the range of 1.2% by weight.

In addition, L. which deteriorates due to the co-addition of Ni and Sn described above. L. C. (Recovery of LLC that has actually been used in automobiles and has deteriorated. The corrosion inhibitor is reduced and the amount of dissolved metals is remarkable.) The effect of improvement is obtained, but this effect is not sufficient if the total amount of Ni and Sn is less than 0.4% by weight, and if it exceeds 2.5%, the hot and cold workability deteriorates. . Therefore, in the present invention, N
0.4 to 2.5% by weight of the sum of the content of i and the content of Sn
Range.

P has the effect of improving the melt castability, the dezincification corrosion resistance and the proof stress.
If the P content is less than 0.001% in weight%, it is not sufficient, and if it exceeds 0.10%, stress corrosion cracking is liable to occur and the hot workability also decreases. Therefore, the content of P in the present invention is in the range of 0.001 to 0.10% by weight.

Further, by the co-addition of Ni and P, Ni
-A P-based compound is formed, which improves strength, proof stress, heat resistance and stress corrosion cracking resistance, and contributes to refining of crystal grains during recrystallization. It has been determined that the weight percentage ratio of Ni / P that can be extracted is in the range of 5-50.

There is a close relationship between the Ni, Sn and P contents and the Zn content, and when the Zn content decreases,
Although the susceptibility to dezincification corrosion and stress corrosion cracking is reduced, the strength becomes insufficient, so that the contents of Ni, Sn and P must be increased. However, when the contents of Ni, Sn and P are increased, the flowability of the molten metal during casting decreases, the deformation resistance increases during hot and cold working, the deformability decreases, or a film is formed during heat treatment. This is disadvantageous in manufacturing. Therefore, the amounts of Ni, Sn and P are the smallest (Ni: 0.1 to 1.5% by weight, Sn: 0.1 to 1.2% by weight).
And P: 0.001 to 0.10% by weight, and the sum of the weight percentages of Ni and Sn is 0.4 to 2.5% by weight, and the ratio of the weight percentage of P to the weight percentage of Ni is in the range of 5 to 50. Zn content (8 to 25% by weight) is the optimum content.

B, when added in a small amount, not only contributes to the deoxidizing effect of the molten metal and to the refinement of the crystal grains during recrystallization, but also to the deterioration L. C. Has the effect of greatly improving the stress corrosion cracking resistance during
If it is less than 0.001%, it is not sufficient, and if it exceeds 0.06%, hot and cold workability deteriorates and it is economically disadvantageous. Therefore, the content of B in the present invention is 0.001 to
It was in the range of 0.06% by weight.

The grain size is preferably 0.005 mm or more because the finer the grain size, the higher the strength and the resistance to stress corrosion cracking. However, when the crystal grain size exceeds 0.030 mm, the strength and the stress corrosion cracking resistance are remarkably reduced, and the surface becomes rough after molding. Therefore, the crystal grain size in the present invention is in the range of 0.005 to 0.030 mm.

In order to cope with thinner radiator tanks, plates and fins, a tensile strength of 35 kgf / mm ² or more,
It is necessary that the Erichsen value be 10 mm or more, and it is preferable that the tensile strength be 36 kgf / mm ² or more and the Erichsen value be 11 mm or more in response to recent demands for weight reduction. Further, in order to reduce the weight of the radiator, it is necessary to improve both strength and moldability. In addition, the above-mentioned improvement of corrosion resistance enables thinning.

The copper-base alloy of the present invention adjusted to the above-described composition has the effect of forming Ni-P compounds and dissolving Ni and dissolving Sn to suppress segregation of Zn and impurities at grain boundaries. As a result, stress corrosion cracking resistance is greatly improved. Therefore, it is possible to use a material having various characteristics required for recent radiator tanks, plates, and fins. In addition, the above-mentioned various characteristics can be advantageously exerted by appropriately controlling the manufacturing conditions when processing a slab through a hot rolling step and a cold rolling step to a desired plate thickness. Hereinafter, the method for producing the copper-based alloy of the present invention will be described in detail.

First, Zn: 8 to 25% by weight,
Ni: 0.1 to 1.5%, Sn: 0.1 to 1.2%, P: 0.001
0.10%, B: 0.001 to 0.06%, and the total of the above-mentioned Ni weight% and Sn weight% is 0.4 to 2.5% by weight, and the ratio of the weight percentage of Ni / P is 5 to 50. Yes, an alloy material consisting of Cu and unavoidable impurities is melt-cast to produce a slab (ingot). It is desirable that the melting and casting be performed in an inert gas atmosphere.
Next, the cast slab is hot-rolled to produce a hot press plate, and descaling is performed.

Next, after the required thickness is reduced by cold rolling, intermediate annealing is performed to obtain recrystallization. If the annealing temperature in this intermediate annealing is lower than 400 ° C, sufficient annealing will not be performed, and the stress corrosion cracking resistance in the final properties will be low. The temperature is preferably from 400 to 650 ° C. because the material becomes coarse and the properties after final annealing deteriorate. If the annealing time in this temperature range is less than 10 minutes, it is difficult to sufficiently remove the strain, so that the subsequent cold rolling step becomes difficult, and
If the length exceeds the range, the crystal grains become coarse and the economy is deteriorated. Therefore, the range of 10 to 600 minutes is preferable.

After the intermediate annealing, the obtained recrystallized product is
Cold rolling is performed to the final sheet thickness at a sheet thickness reduction rate of%. This is because if the thickness reduction rate is less than 20%, the residual internal stress imparted by the processing is too small, and the strength and hardness in the final properties after the final annealing step of the subsequent recrystallization cannot be sufficiently improved, and the 70% When rolling exceeds, due to the development of rolling texture,
Since mechanical properties have directionality (anisotropic), thereby reducing formability and increasing residual internal stress, sufficient processing can be performed in the final annealing step of recrystallization later. This is because the stress corrosion cracking resistance is reduced.

Next, the recrystallization after the cold rolling is carried out at 400 to 7
Anneal at a temperature of 00 ° C for 1 to 300 minutes. If the annealing temperature is lower than 400 ° C., sufficient annealing cannot be performed, and the properties, stress corrosion cracking resistance and formability decrease. If the temperature exceeds 700 ° C., a desired crystal grain size cannot be obtained ( The crystal grain size is increased), and the strength, proof stress, hardness and stress corrosion cracking resistance are reduced. If the annealing time in this temperature range is less than 1 minute, sufficient annealing cannot be performed, and a considerable amount of internal stress generated in the cold rolling step, which is the previous step, remains, resulting in forming workability and stress resistance. Since the corrosion cracking property is reduced and the economy is impaired for a long time exceeding 300 minutes, the range of 1 to 300 minutes is preferable.

Next, the alloy sheet obtained after the above recrystallization annealing is further cold-rolled at a sheet thickness reduction rate of 1 to 15%, more preferably 3 to 10%, and then at a temperature of 100 to 400 ° C. In 5
Perform low temperature annealing for ~ 600 seconds. This is done to improve the strength, stress corrosion cracking resistance and caulking (proof strength), and caulking is one of the comparative concepts of the ability of a material to adapt to forming a certain shape. This is a characteristic that greatly depends on the proof stress value. Therefore, if the rate of reduction in sheet thickness in cold rolling is less than 1%, it is difficult to control the sheet thickness, and improvement in properties cannot be expected. If it exceeds 15%, the residual internal stress increases, and subsequent low-temperature annealing Is not improved, and the stress corrosion cracking resistance is reduced. Therefore, the range is set to 1 to 15%.

On the other hand, the annealing temperature in the low-temperature annealing is 100
If the temperature is lower than ℃, sufficient recovery is not performed, the internal stress generated by the above cold rolling remains considerably, and the stress corrosion cracking resistance and molding workability decrease.If the temperature exceeds 400 ° C, the strength, proof stress and hardness are reduced. Since the temperature is lowered, the temperature is set in the range of 100 to 400 ° C. If the annealing time at the annealing temperature is less than 5 seconds, a sufficient effect of low-temperature annealing does not appear, and if it exceeds 600 seconds, the strength, proof stress and hardness are reduced, and it is not preferable from the economical viewpoint. The range was ~ 600 seconds.

By performing the working and heat treatment as described in detail above, particularly the cold rolling and the low-temperature annealing after the final recrystallization annealing, the Ni-P-based compound is uniformly and finely formed in the crystal grain boundaries and in the crystal grains. A thin plate of a copper-based alloy having a dispersed structure can be obtained. In addition, since this copper-based alloy is excellent in strength, caulking property (proof stress), deep drawability (Erichsen value), and stress corrosion cracking resistance, a radiator for an automobile (lightening and high reliability can be achieved). ) And various other industrial or domestic heat exchangers. Further, it can be sufficiently used as a material for electric and electronic parts.

Hereinafter, the present invention will be described in more detail with reference to examples. However, the scope of the present invention is not limited by the following examples.

[0031]

EXAMPLES Alloy materials (sample Nos. 1 to 19: Nos. 1 to 6 are materials of the alloy of the present invention, and Nos. 7 to 17 are materials of comparative alloys) whose chemical component values (% by weight) are shown in Table 1. Nos. 18-19 are melted using a conventional high-frequency melting furnace, and a 40mm × 40
It was cast into an ingot of mm × 140 mm. The melting was performed by completely shielding the melting and casting atmosphere with an inert gas.

[0032]

[Table 1] Next, each ingot was chamfered and then cut into a size of 40 mm × 40 mm × 15 mm, and the slab was hot-rolled at 810 ° C. to obtain a hot-rolled sheet having a thickness of 5 mm. Cold rolled to 1.5mm, 500
Annealed at a temperature of ~ 550 ° C. After annealing, this is quenched with water, further pickled, and then cold rolled to a thickness of 0.55 mm.
Annealing was performed at a temperature of 0 ° C. so that the crystal grain size became 0.025 mm. However, the sample of No. 17 was annealed at 650 ° C,
0.060 mm. The crystal grain size was determined with reference to JIS H0501.

Next, these samples were cold-rolled to 0.51 mm (deformation ratio: 7.3%), and were annealed at 100 to 400 ° C. for 100 to 600 seconds (the sample of No. 17 was a 0.060 mm crystal). The grain size and the grain size of the other samples were set to 0.025 mm). After the low-temperature annealing, the obtained plate material was pickled and buffed to adjust the surface roughness to Rmax 1.5 μm or less. In addition,
The tensile strength, elongation, Erichsen value and stress corrosion cracking resistance of each sample obtained here were examined, and the results are shown in Table 1.

The measurement of tensile strength, elongation and Erichsen value was carried out according to JIS Z 2241 and JIS Z 2247 (Method A), respectively. Regarding the resistance to stress corrosion cracking, commercially available ammonia water (25 to 28%) was diluted with pure water, and a solution of about 13% was poured into the bottom of the desiccator. Then, the stress at the center was 10 kgf /
The test specimen bent in an arch shape to ² mm was placed in a desiccator together with its holder in a desiccator, kept at room temperature, and after each predetermined time, these test specimens were taken out of the desiccator and thoroughly washed with water. After performing the test, the surface of the test piece is
Observation was performed at a magnification of 40 times, and the crack generation time was measured.

As an evaluation of the resistance to stress corrosion cracking, the deterioration of the L.A. L. C. After immersing the arched test piece in (Long Life Coolant) and keeping it at 70 to 90 ° C for 300 hours,
After a lapse of 00 hours, these test pieces were taken out, washed sufficiently with water, and the surface of the test piece was magnified 40 times with a stereoscopic microscope to check for cracks. The results are also shown in Table 1. In Table 1, circles indicate that only surface discoloration did not cause cracks, triangles indicate that no cracks occurred but corrosion was remarkable, and crosses indicate that cracks occurred. Are shown.

The deterioration L. L. C. Is an extremely reliable and effective method for judging the characteristics as a constituent material of a radiator for an automobile.

From the results in Table 1, the following has been found.
The alloys of samples No. 1 to No. 6, which are preferred embodiments of the present invention,
It has excellent tensile strength, elongation, Erichsen value, workability and solderability, and good stress corrosion cracking resistance (L.
L. C. It also has good stress corrosion cracking resistance to the internal environment in contact with the metal) and is inexpensive without using a large amount of expensive metal. Therefore, it turns out that it is a very excellent alloy as a constituent material of all heat exchangers including radiators for automobiles.

On the other hand, the sample of Sample No. 7 in which Zn is smaller than the amount specified in the present invention has low strength and expensive Cu.
Since the content is large and the raw material cost rises, it is understood that it is unsuitable as an industrial material. Conversely, Ni, Sn,
P and B are the amounts specified in the present invention, but the sample of Sample No. 8 in which Zn is larger than the amount specified in the present invention can be manufactured because cracks occur during hot rolling. Did not.

The sample of sample No. 9 containing no B and the sample of sample No. 10 in which B is smaller than the amount specified in the present invention are as follows:
Low strength and poor stress corrosion cracking resistance. Sample No. 11 in which B is larger than the amount specified in the present invention cracked during hot rolling. In addition, the sample No. 12 containing no Sn has low strength, elongation and stress corrosion cracking resistance, and the sample No. 13 not containing Ni also has low strength, elongation and stress corrosion cracking resistance. It turns out that it is inferior. On the other hand, each component of Zn, Ni, Sn, P and B is the amount specified in the present invention, but the amount of Ni + Sn is small, and the ratio of the weight% of P to the weight% of Ni is smaller than the value specified in the present invention. It can be seen that the sample of Sample No. 14 has low strength, elongation and low stress corrosion cracking resistance. Also,
Sample No. in which the amount of Ni + Sn is larger than the amount specified in the present invention.
The 15 sample cracked during hot rolling,
Could not be manufactured.

The sample of sample No. 16 in which the ratio of the weight percentage of P to the weight percentage of Ni is higher than the value specified in the present invention, has low strength and poor stress corrosion cracking resistance. Also, Zn,
Ni, Sn, P, B, each component and amount of Ni + Sn, Ni
Even when the / P ratio is the amount specified in the present invention, the sample of sample No. 17 having a large crystal grain size is inferior in strength, elongation and stress corrosion cracking resistance. Further, Sample No. 18 in which B was added to a conventional brass material containing no Ni, Sn and P, and
The sample No. 19 is inferior in both strength and stress corrosion cracking resistance, and it is difficult to improve stress corrosion cracking resistance only by adding B, and Ni, Sn, P
It is understood that co-addition is essential.

[0041]

As described above, the copper-based alloy according to the present invention comprises:
As a constituent material of a heat exchanger, particularly a radiator for an automobile, strength, moldability and stress corrosion cracking resistance (LL.
C. (Including stress corrosion cracking resistance to the internal environment that comes into contact with), and is sufficient for the weight reduction, high reliability, and low cost of heat exchangers recently desired in various fields. It can respond to.

Continuation of the front page (72) Inventor Mitsuhiro Kosaka 1-8-2 Marunouchi, Chiyoda-ku, Tokyo Dowa Mining Co., Ltd. (56) References JP-A-3-193849 (JP, A) JP-A-5-312992 ( JP, A) JP-A-5-311295 (JP, A) JP-A-61-542 (JP, A) JP-A-62-30861 (JP, A) (58) Fields investigated (Int. Cl. ⁷ , (DB name) C22C 9/04 C22F 1/08

Claims (4)

(57) [Claims] 1% by weight of Zn: 8 to 25%;
i: 0.1 to 1.5%, Sn: 0.1 to 1.2%, P: 0.001 to
0.10%, B: 0.001 to 0.06%, and the total of the above-mentioned Ni weight% and Sn weight% is 0.4 to 2.5% by weight, and the ratio of the weight percentage of Ni / P is in the range of 5 to 50. ,
Balance Ri Do Cu and inevitable impurities, Ni-P-based
Heat exchanger copper base alloy you characterized in that the compound is uniformly dispersed. 2. The copper base alloy for a heat exchanger according to claim 1, wherein the crystal grain size is 0.005 to 0.030 mm. 3. The copper base alloy for a heat exchanger according to claim 1, wherein the copper base alloy has a tensile strength of 35 kgf / mm ² or more and an Erichsen value of 10 mm or more. 4. The composition according to claim 1, wherein Zn: 8 to 25%,
i: 0.1 to 1.5%, Sn: 0.1 to 1.2%, P: 0.001 to
0.10%, B: 0.001 to 0.06%, and the total of the above-mentioned Ni weight% and Sn weight% is 0.4 to 2.5% by weight, and the ratio of the weight percentage of Ni / P is in the range of 5 to 50. ,
An alloy material consisting of Cu and unavoidable impurities with the balance being 20
After cold rolling at a thickness reduction rate of ~ 70%, recrystallization is performed, and after the final annealing of this recrystallization , cold rolling is performed at a thickness reduction rate of 1 to 15%, and at a temperature of 100 to 400 ° C. A method for producing a copper-based alloy for a heat exchanger, wherein low-temperature annealing is performed for 5 to 600 seconds.