JPH10310855A - Production of precipitation hardening type copper alloy bar - Google Patents

Abstract

PROBLEM TO BE SOLVED: To produce an extremely thin precipitation-hardening type copper alloy bar having high strength. SOLUTION: This method has a solution treating stage in which, while a bar stock Ti with <=0.5 mm thickness composed of a precipitation hardening type copper alloy is run, this bar stock T1 is continuously subjected to rapid heating to the solid solution temp. of the precipitation hardening type copper alloy, and, successively, the rapidly heated bar stock is rapidly cooled and a precipitation hardening stage in which the rapidly cooled bar stock T2 heated and is subjected to precipitation hardening. The temp. rizing rate of the bar stock T1 from 300 deg.C in the rapid heating to the solid solution temp. is regulated to >=40 deg.C/sec, the holding time at >=600 deg.C is regulated to 1 to 60 sec, and the temp. dropping rate from the solid solution temp. to 300 deg.C in the rapid cooling is regulated to >=40 deg.C/sec.

Description

DETAILED DESCRIPTION OF THE INVENTION

[0001]

BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a method for producing an ultra-thin, high-strength precipitation hardening type copper alloy strip.

[0002]

2. Description of the Related Art Recently, as electric and electronic products have been used in various environments, the use conditions of electronic parts, lead frame materials, and conductive parts of terminal connectors have tended to be severe. Yes, there is a strong demand for metal materials that are thinner and stronger than before, have high electrical and thermal conductivity, and also have properties according to applications such as spring properties, slip properties, plating properties, and corrosion resistance. I have.

As a metal material that can meet such a demand, the present applicants have paid attention to a precipitation hardening type copper alloy. Precipitation hardening type copper alloy is a copper alloy containing a precipitation hardening element.The solid solution curve is obtained by heating a solid solution temperature determined by the material to form a solid solution of the precipitation hardening element in a supersaturated state. By holding at a lower temperature for a certain time,
It is characterized in that fine particles of the intermetallic compound precipitate on the crystals of the saturated solid solution, whereby precipitation hardening can be achieved. For example, in the case of a typical 0.1% Zr—Cu alloy, the solution is heated to 940 ° C. to make Zr a supersaturated solid solution, and then maintained at a temperature of about 400 to 500 ° C. for about 3 hours. By doing so, fine particles of ZrCu are precipitated and the strength is increased.

[0004]

This kind of precipitation hardening type copper alloy has extremely high strength and is expected to be used for various purposes as a thin plate. Therefore, it is difficult to obtain a thin plate due to high processing efficiency, and there is a problem that even if processing can be performed, sufficient strength and quality cannot be ensured. For example, in a conventional method of manufacturing a precipitation hardening type copper alloy material, after performing a solution treatment on a relatively thick, for example, about 2 to 15 mm precipitation hardening type copper alloy material, further rolling to a product thickness, and then The product was subjected to a precipitation hardening process, but the product was, for example, 0.1%.
When the thickness is as thin as 25 mm, it is necessary to perform high-strength hot rolling after the solution treatment, and a problem has been found that the effect of precipitation hardening is reduced.

The present invention has been made in view of the above circumstances, and it is an object of the present invention to enable production of an ultrathin, high-strength precipitation hardening type copper alloy strip.

[0006]

In order to solve the above-mentioned problems, a method of manufacturing a precipitation hardening type copper alloy strip according to the present invention is to run a strip hardening copper alloy strip having a thickness of 0.5 mm or less. While rapidly heating the strip material above the solution temperature of the precipitation hardening type copper alloy, and then rapidly cooling the rapidly heated strip material, A precipitation hardening step of heating and precipitating and hardening the strip, wherein the rate of temperature increase of the strip from 300 ° C. to the solution temperature in the rapid heating is 40 ° C./sec or more, and 600 The holding time of the strip above ℃ is 1 ~
60 seconds, and the rate of temperature decrease from the solution temperature to 300 ° C. in the rapid cooling is 40 ° C./sec or more.

[0007]

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS An embodiment of a method for producing a precipitation hardening type copper alloy strip according to the present invention will be described below. In the method of this embodiment, first, a strip material having a thickness of 0.5 mm or less made of a precipitation hardening type copper alloy is manufactured by rolling (rolling step). Next, while the strip is running, it is continuously and rapidly heated to a temperature equal to or higher than the solution temperature of the precipitation hardening type copper alloy, and then the rapidly heated strip is continuously and rapidly cooled to perform a solution treatment. (Solution treatment step). Further, the strip material subjected to the solution treatment is heated again to precipitate and harden, and subjected to a precipitation hardening treatment (precipitation hardening process). Although the type of precipitation hardening type copper alloy to which the present invention can be applied is not limited, examples of preferable alloy compositions are listed in Table 1, and the respective solution temperatures are also described.

[0008]

[Table 1]

[Rolling Step] First, in the rolling step, a precipitation hardening type copper alloy material obtained by casting is hot or / and cold rolled to obtain a strip having a thickness close to that of a final product. Specifically, at this stage, rolling is performed to a thickness of 0.5 mm or less, more preferably 0.3 mm or less, and still more preferably 0.2 mm or less. If the thickness is more than 0.5 mm, continuous rapid heating and continuous rapid cooling of the strip material in the next solution treatment step become difficult, and crystals may grow during the temperature rise and the crystal structure may become coarse. At the same time, the thickness after rolling is desirably not more than twice the thickness of the final product. The lower limit thickness of the strip subjected to the solution treatment is not particularly limited, but is practically 0.0
It is considered to be about 7 mm. Although the rolling conditions are not particularly limited, it is generally preferable to perform hot rolling or cold rolling at about 800 to 980 ° C. The rolled material after rolling may be wound on a recoiler or the like and transferred to the next step, or may be continuously flowed to the next step.

[Solution treatment step] In the solution treatment step,
While continuously running the strip, the strip is rapidly heated by a continuous heating furnace to the solution temperature of the precipitation hardening type copper alloy,
The precipitation hardening element is supersaturated in the mother phase and then rapidly cooled, so that the solution hardened precipitation hardening element is not deposited.

In the rapid heating, the rate of temperature rise of the strip in the range from 300 ° C. to the solution temperature is 40 ° C./sec or more, more preferably 60 ° C./sec or more, and further preferably 100 ° C./sec.
/ Sec or more. If the temperature is lower than 40 ° C./sec, there is a problem that the structure becomes coarse due to crystal growth. Similarly, in the rapid cooling, the rate of temperature reduction of the strip in the range from the solution temperature to 300 ° C. is 40 ° C./sec or more, more preferably 60 ° C.
/ Sec or more, more preferably 100 ° C / sec or more. If it is lower than 40 ° C./sec, the structure tends to be coarse.

600 ° C. of the strip during the solution treatment step
The above holding time needs to be 1 to 60 seconds, and more preferably 1 to 20 seconds. If it is shorter than 1 second, it is difficult to sufficiently form a solution. If it is longer than 60 seconds, crystals may grow and the crystal structure may be coarse.

FIG. 1 shows an example of a solution treatment apparatus that can be used in a solid solution treatment step. However, the invention is not limited to the use of this device only, and other types of continuous heating furnaces can be used as well. Solution treatment equipment 1
, A strip material T1 before solution treatment manufactured by rolling is horizontally fed out from an uncoiler (not shown) or the like, and the path is changed upward by a guide roll 2 and introduced into the heating chamber 4. Although not shown, a sealing means is provided at the entrance to the heating chamber 4, and the heating chamber 4 is hermetically closed.

A heating roll 6 is arranged in the heating chamber 4 with its axis being horizontal. The heating roll 6 is rotated by a driving mechanism (not shown) in accordance with the running speed of the strip T1. In the heating chamber 4, an inert gas such as nitrogen or argon,
A reducing gas such as hydrogen or carbon monoxide, or a mixed gas thereof is supplied, and is kept in an inert or reducing atmosphere.

A heating means such as electric heating or combustion heat is provided inside the heating roll 6.
The outer peripheral surface temperature of the heating roll 6 is heated to a certain temperature equal to or higher than the solution temperature of the precipitation hardening type copper alloy T1. According to the method in which the heating roll 6 is brought into contact with the strip material T1 and heated, the heat transfer efficiency is 5 times or more as compared with a normal heating furnace, and rapid heating that is difficult with a normal heating furnace is possible. Not only that, the heat transfer is performed evenly over the entire area of the strip T1, so that uniform heating is possible, and the tension applied to the strip T1 during heating is easily adjusted accurately. For this reason, it is particularly suitable as a heating means of the present invention for a thin plate of a difficult-to-process material. The heating chamber 4 may also be provided with auxiliary heating means such as a burner or a high-frequency induction heating device.

Although the material of the heating roll 6 is not limited, it is generally desirable that the heating roll 6 is formed of a metal having excellent heat resistance, and the outer peripheral surface thereof is mirror-finished so as to be in close contact with the strip T1. Is preferred. Heating roll 6
The outer diameter of is not limited in the present invention, but easy to heat,
In consideration of the thickness and running speed of the strip T1 to be treated, it is generally about 50 to 100 cm, more preferably 60 to 90 c.
m.

The rotation speed of the heating roll 6 is not limited, but is desirably set to a speed slightly higher than the feeding speed of the strip T1 from an uncoiler or the like, and specifically, 0.1 to 10%. Hopefully it will be faster. This is because the strip T1 gradually heat-expands in the process of contacting the strip T1 with the outer periphery of the heating roll 6 and increasing the temperature, and loosens between the heating roll 6 and the strip T1 before solid solution. This is because peeling may occur. When such peeling occurs, heat conduction from the heating roll 6 to the strip T1 is hindered, and the strip T
Since the temperature of (1) becomes non-uniform, it must be avoided as much as possible.

In the illustrated example, the strip T1 is wound around the outer peripheral surface of the heating roll 6 by a central angle of 180 °, and the other end of the strip T1 extends vertically downward. Thereby, the strip T1
Adheres over a large area to the heating roll 6 and is rapidly heated by direct heat conduction until the temperature becomes substantially equal to the outer peripheral surface temperature of the heating roll 6, so that the strip material T1 is uniformly and high even at a high line speed. Heating can be performed with precision. In addition, the heating method using the roll abutment has several times higher thermal efficiency than the vapor-phase heating method, so that not only the heating cost is reduced, but also the tension applied to the strip T1 in the heating process by the heating roll 6 is made uniform. Since the adjustment can be performed, the thin strip T1 can be uniformly heated to a high temperature without being deformed. Therefore, the heating method by roll contact is particularly suitable for the present invention in which the solution is rapidly heated to a solution temperature of 700 ° C. or higher.

A cooling chamber 10 is provided below the heating chamber 4, and the strip T 1 passes through the cooling chamber 10. A large number of cooling nozzles 12 are arranged in the cooling chamber 10 so as to face each of the front and back surfaces of the strip T1, and a cooling medium such as cooling water or a cooling gas sent from a supply mechanism (not shown) is supplied to the cooling nozzles. 12 is sprayed on the strip T1. According to this configuration, the strip T1 once heated to the solution temperature or higher can be rapidly cooled and crystal growth can be prevented, so that the crystal grain size in the solidified strip T2 is sufficiently reduced (for example, 5 to 15 μm).

An opening 10A at the lower end of the cooling chamber 10 is disposed in a cooling water tank 14, immersed in a cooling liquid circulated and supplied to the cooling water tank 14, and is airtightly closed. Thereby, the inside of the heating chamber 4 and the cooling chamber 10 is maintained in an inert atmosphere or a reducing atmosphere. After the cooling roll 16 is immersed in the cooling liquid and sufficiently cooled by the cooling liquid, the solution-dissolved strip T2 is sent upward by the cooling roll 16. The solution-dissolved strip T2 sent out is wound into a coil by a recoiler via an unillustrated pickling device, water washing device, drying device and the like.

As the cooling liquid in the cooling water tank 14, ordinary water can be used, but more preferably, an aqueous solution of a free oxygen inhibitor is used. The free oxygen inhibitor is an agent for removing oxygen in water, and hydrazine is an example. The concentration of the free oxygen inhibitor is 5 to 30 wt%
Degree is fine. By adding the free oxygen inhibitor, it is possible to effectively suppress the oxidation of the surface of the solution-dissolved strip T2.

FIG. 2 shows a modification of the solution treatment apparatus 1.
In the solution treatment apparatus 1, a first heating roll 6A and a second heating roll 6B are arranged in a heating chamber 4 in parallel, and a strip T
1 is the lower side of the first heating roll 6A and the second heating roll 6
It is characterized by being wound above B. Other configurations are the same as those of the apparatus shown in FIG.

According to the solution treatment apparatus 1 of FIG. 2, after preheating the strip T1 with the first heating roll 6A,
The main heating can be performed by the second heating roll 6B. In this case, the outer peripheral surface temperatures of the first heating roll 6A and the second heating roll 6B may be the same or different. For example, while the temperature of the first heating roll 6A is set to a temperature lower than the solution temperature, the temperature of the second heating roll 6B can be set to be higher than the solution temperature. According to such a method, it is possible to secure a large total contact area between the strip T1 and the rolls 6A and 6B.
Even when the running speed of is increased, it is possible to heat sufficiently uniformly. Even when the thickness of the strip T1 is relatively large, there is an advantage that uniform heating is easy.

In the apparatus shown in FIG. 2, the strip material T1 is heated by the first roll 6A to the solution temperature or higher while the second roll 6A is heated.
Precooling with B is also possible. In this case, a cooling medium such as cooling water may be circulated and supplied inside the second roll 6B. By arranging the cooling roll 6B adjacent to the heating roll, there is an advantage that the strip T1 on which the solution treatment has been completed can be cooled more quickly.

[Rolling Step After Solution Treatment] The strip material T2 after the solution treatment may be rolled before or after the precipitation hardening treatment. Actually, it is preferable to perform appropriate rolling at least at any point, since the stress of the solution-solution strip can be released. When rolling is performed before the precipitation hardening treatment, the rolling reduction is preferably 4 to 90%, more preferably 20 to 60%, and when the rolling is performed after the precipitation hardening treatment, the rolling reduction is The cold rolling is preferably 5 to 60%, more preferably 30 to 50%.
In any case, when the rolling reduction is less than the lower limit, the stress cannot be released, and the crack limit value relatively decreases. On the other hand, when the rolling ratio is larger than the upper limit, the strip material after rolling has directionality and is easily cracked.

[Precipitation-hardening treatment step] The solid-solution strip material T2
Is then subjected to a precipitation hardening step. In this step,
It is an object of the present invention to hold the solution-treated strip material T2 at a temperature lower than the solid solubility curve for a certain period of time to precipitate fine particles of the intermetallic compound on the crystals of the saturated solid solution, thereby achieving precipitation hardening.

In the precipitation hardening treatment, the solution-treated strip T2 is
The heating is performed by heating to 50 to 600 ° C, more preferably 300 to 600 ° C, and the heating time is 0.1 to 10 hours.
More preferably, it is set to 0.5 to 5 hours.

FIG. 3 shows an example of a heating device (annealing furnace) suitable for the precipitation hardening step. The annealing furnace 20 is a so-called bell-type annealing furnace, and has a feature that the heating temperature can be controlled with higher precision than a general continuous annealing furnace. However, the precipitation hardening step in the present invention can be performed even by using a general continuous annealing furnace or another heating furnace.

[0029] A solution-solubilized strip T2 wound in a coil shape
Are coaxially stacked and are airtight metal inner containers 2
2, the inside of the inner container 22 is filled with an inert gas such as nitrogen or argon or a reducing gas such as hydrogen or carbon monoxide. Among them, it is particularly preferable to use hydrogen gas. This is because the thermal conductivity is good and the specific gravity is light, so that the power consumption for circulation can be reduced. A circulation fan 28 is provided below the inner container 22, and the circulation fan 28 circulates gas as shown by the arrow in the figure. The inner container 22 is further housed in an outer container 24, in which a number of heating means such as a burner 26 for heating the inner container 22 from the outside are provided. When the inner container 22 is heated by the burners 26, the gas inside the inner container 22 is heated, and the solution-solidified strip T2 is uniformly heated as the gas is circulated by the circulation fan 28.

By performing the precipitation hardening treatment under the above-described conditions using the above-described annealing furnace 20, fine particles of the intermetallic compound are precipitated on the crystals of the saturated solid solution, whereby the precipitation hardening can be achieved. is there. When the precipitation hardening process is completed, the outer container 24 and the inner container 22 are opened, the strip T2 is taken out, and if necessary, the aforementioned rolling is performed to obtain a product.

According to the method for producing a precipitation hardening type copper alloy strip as described above, after rolling to a thickness close to the final thickness of the product to produce a precipitation hardening type copper alloy strip T1, the thin strip material T1 Is rapidly heated to a solution temperature and rapidly cooled, so that the precipitation hardening state is well maintained even in the final product state, and the original high strength of the precipitation hardening type copper alloy is obtained.

In particular, in this embodiment, the heating roll 6 heated to a temperature equal to or higher than the solution temperature is brought into contact with the strip T1,
Since the configuration is such that the strip T1 is heated by heat conduction, the strip T1 can be uniformly heated to a temperature that accurately reflects the outer peripheral surface temperature of the heating roll 6 in combination with the thinness of the strip T1. Therefore, the precipitation hardening state can be accurately controlled, and the line speed can be increased. Furthermore, since the strip T1 is heated while being supported by the heating roll 6, the strip T1 is unlikely to be deformed in a wavy shape or the like, and the shape accuracy of the final product is improved despite heating in a thin state.

The strip T1 heated to the solution temperature
On the other hand, since cooling is performed by spraying cooling water or the like from the cooling nozzle 12 immediately, the thickness of the strip T1
Can be rapidly cooled. Therefore, crystal growth during cooling can be suppressed, and coarsening of the crystal grain size can be prevented. Also from this point, the original high strength of the precipitation hardening type copper alloy can be obtained. Further, since the configuration is such that conduction heating is performed by the heating roll 6, the entire apparatus can be reduced in size as compared with a configuration in which a plurality of burners are arranged, space can be saved, and running costs of inert gas and the like can be reduced. .

[0034]

EXAMPLES Next, the effects will be demonstrated with reference to examples of the present invention. Using three types of precipitation hardening type copper alloys A to C having the following compositions (all wt%), a precipitation hardening type copper alloy strip is manufactured by the method of the example according to the present invention and the method of three types of comparative examples, respectively. And compared the characteristics.

Alloy A (solution temperature: 750 ° C.): 2.5% Ni—0.65% Si—0.05% Mg—balance Cu Alloy B (solution temperature: 750 ° C.): 2.0% Ni-0 0.5% Si-0.5% Sn-balance Cu alloy C (solid solution temperature 850 ° C): 0.02% Si-0.3% Cr-0.1% Zr-0.1
% Mg-balance Cu

[Examples] Cast ingots each having a thickness of 150 mm and a width of 540 mm were prepared using alloys A to C. After homogenizing the cast ingot at 900 to 960 ° C. for 2 hours, a thickness of 11 mm was obtained while performing a solution treatment by hot rolling.
And cooled using cooling water. After the surface of the obtained sheet material was chamfered, cold rolling and annealing below the solution temperature were repeated to prepare a strip material having a thickness of 0.2 mm and a width of 200 mm.

Next, using the apparatus shown in FIG. 1, these strips were rapidly heated to their respective solution temperatures, and further quenched with cooling water for solution treatment. At that time, the rate of temperature rise from 300 ° C. to the solution temperature was about 150 ° C./sec, and the rate of temperature decrease from the solution temperature to 300 ° C. was about 150 ° C./sec. The running speed of the strip during the solution treatment was all 20 m / min.
As the heating roll 6, a roll with a built-in metal burner having an outer diameter of 750 mm was used.

The strip after solution treatment was cold-rolled at a rolling reduction of 20% to a thickness of 0.16 mm and wound into a coil. The wound coil was housed in a bell-type annealing furnace 20 as shown in FIG. 3 and subjected to a precipitation hardening treatment at 450 ° C. for 3 hours.

Comparative Example 1 Cast ingots each having a thickness of 150 mm and a width of 540 mm were prepared using alloys A to C. After homogenizing the cast ingot at 900 to 960 ° C. for 2 hours, the thickness is 11 m while performing a solution treatment by hot rolling.
m and cooled with cooling water. After the surface of the obtained plate material was chamfered, cold rolling and annealing below the solution temperature were repeated to prepare a strip material having a thickness of 0.16 mm and a width of 200 mm.

Comparative Example 2 Cast ingots each having a thickness of 150 mm and a width of 540 mm were prepared using alloys A to C. After homogenizing the cast ingot at 900 to 960 ° C. for 2 hours, it was hot-rolled to a thickness of 11 mm and cooled using cooling water. After chamfering the surface of the obtained sheet material, cold rolling and annealing below the solution temperature were repeated to a thickness of 1.0 mm.
Was prepared and wound into a coil. The coils were heated to respective solution temperatures in an annealing furnace under an inert gas atmosphere, and the heated coils were cooled by the inert gas. In this case, the rate of temperature rise from 300 ° C. to the solution temperature is about 0.2 ° C./sec, and the rate of temperature decrease from the solution temperature to 300 ° C. is about 0.1 ° C./sec. This strip is subjected to cold rolling to prepare a strip having a thickness of 0.16 mm and a width of 200 mm. After winding the strip in a coil shape, the strip is placed in a bell-type annealing furnace 20 and heated at 450 ° C. × 3. The precipitation hardening treatment was performed under the condition of time.

Comparative Example 3 Casting ingots each having a thickness of 150 mm and a width of 540 mm were prepared using the alloys A to C. After homogenizing the cast ingot at 900 to 960 ° C. for 2 hours, it was hot-rolled to a thickness of 11 mm and cooled using cooling water. After chamfering the surface of the obtained sheet material, cold rolling and annealing below the solution temperature were repeated to a thickness of 1.0 mm.
Were prepared, heated to the respective solution temperatures through a continuous annealing furnace while running the strip, and then continuously quenched with cooling water. In this case, the rate of temperature rise from 300 ° C. to the solution temperature is about 15 ° C./sec, and the rate of temperature decrease from the solution temperature to 300 ° C. is about 15 ° C./sec.
Thereafter, the strip is cold-rolled to a thickness of 0.16 mm.
After winding in a coil shape, it was placed in a bell-type annealing furnace 20 and subjected to a precipitation hardening treatment at 450 ° C. × 3 hours.

[Test Method] The three types of precipitation hardening type copper alloy strips obtained by each method were subjected to electric conductivity measurement, tensile strength measurement, elongation measurement, crystal grain size measurement, W bending test, and plating. Sex tests were performed respectively.

In the W bending test, a 10 mm × 60 mm test piece was cut out from each alloy strip, and when each test piece was bent by 90 °, the minimum inner radius (R) at which the outer surface of the bent portion did not have rough skin was determined. , The value divided by the thickness (T) of the test piece (R /
T). That is, the smaller the R / T value, the better the bendability.

The plating properties were as follows: a test piece cut from a strip was electroplated with silver to a thickness of 2 μm, and this
Evaluation was made based on the density of blisters generated on the plating surface when heated at 50 ° C. for 5 minutes (pieces / 100 mm ² ).
Those of 0mm ² "◎", those of one / 100mm ² "○", those of two / 100mm ² "△", was evaluated those of three or more / 100mm ² as "×". Alloy A
Are shown in Table 2, the result of Alloy B is shown in Table 3, and the result of Alloy C is shown in Table 4.

[0045]

[Table 2]

[0046]

[Table 3]

[0047]

[Table 4]

As is apparent from Tables 2 to 4, in any of the alloys, the strip obtained by the method of the embodiment is as follows.
Plating properties, bending properties, and tensile strength were superior to the strips obtained by the methods of Comparative Examples 1 to 3. In addition, there was no inferiority in electric conductivity and elongation, and the crystal grain size was small.

[0049]

As described above, according to the method of manufacturing a precipitation hardening type copper alloy strip according to the present invention, a thin strip near the final thickness of a product is heated to a solution temperature, and further quenched. Therefore, the precipitation hardening state is favorably maintained even in the state of the final product, and the original high strength of the precipitation hardening type copper alloy can be obtained.

[Brief description of the drawings]

FIG. 1 is a schematic view showing an example of a solution treatment apparatus used in a method for producing a precipitation hardening type copper alloy strip according to the present invention.

FIG. 2 is a schematic view showing a modified example of the solution treatment apparatus.

FIG. 3 is a schematic view showing an example of a precipitation hardening apparatus used in the method of the present invention.

[Explanation of symbols]

 DESCRIPTION OF SYMBOLS 1 Solution treatment apparatus 4 Heating chamber 6 Heating roll 6A 1st heating roll 6B 2nd heating roll 10 Cooling chamber 12 Cooling nozzle 16 Cooling roll T1 strip T2 Solution-processed strip

──────────────────────────────────────────────────続 き Continuation of the front page (51) Int.Cl. ⁶ Identification code FI C22F 1/00 630 C22F 1/00 630A 684 684A 685 685Z 691 691A 691B 691C 692 692Z 694 694A

Claims (5)

[Claims] 1. A thickness of 0.5 m made of a precipitation hardening type copper alloy
m, while rapidly moving the strip material to a temperature equal to or higher than the solution temperature of the precipitation hardening type copper alloy, and then rapidly cooling the rapidly heated strip material. And a precipitation hardening step of heating the rapidly cooled strip to precipitate and harden the strip, wherein the rate of temperature increase of the strip from 300 ° C. to the solution temperature in the rapid heating is 40 ° C. / And the holding time at 600 ° C. or more is 1 to 60 seconds, and the cooling rate from the solution temperature to 300 ° C. in the rapid cooling is 40 ° C./sec or more. Manufacturing method of precipitation hardening type copper alloy strip. 2. The method according to claim 1, further comprising: a rolling step of rolling the rapidly cooled strip at a rolling rate of 4 to 90%, wherein the precipitation hardening step is performed after the rolling step. 2. The method for producing a precipitation hardening type copper alloy strip according to item 1. 3. The strip material that has undergone the precipitation hardening treatment step is prepared as follows.
The method for producing a precipitation hardening type copper alloy strip according to claim 1 or 2, further comprising a rolling step of rolling at a rolling rate of 60%. 4. The method according to claim 1, further comprising, before the solution treatment step, a rolling step of rolling the precipitation hardening type copper alloy material to obtain the strip material having a thickness of 0.5 mm or less.
4. The method for producing a precipitation hardening type copper alloy strip according to any one of items 1 to 3. 5. The precipitation according to claim 1, wherein, in the precipitation hardening step, the solution-treated strip is kept at 250 to 600 ° C. for 0.1 to 10 hours. Manufacturing method of hardening type copper alloy strip.