JP2016145398A - High strength coated aluminum alloy material for brazing and connector material excellent in screw strength - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a high strength coated aluminum alloy and a connector member having excellent processability before brazing and capable of securing high strength in a short time after brazing.SOLUTION: A high strength coated aluminum alloy and a connector member consists of, by mass%, Mn:0.50 to 1.30%, Mg:0.30 to 0.60%, Zn:4.5 to 6.5%, Fe:0.10 to 0.30% and further one or two kinds from Ti:0.01 to 0.20% and Bi:0.01 to 0.20% if desired and the balance Al with inevitable impurities.SELECTED DRAWING: Figure 1

Description

  The present invention relates to a high-strength processed aluminum alloy material for brazing that has been subjected to brazing and has high strength after brazing, and a connector material excellent in screw strength.

Automotive heat exchangers such as radiators, condensers, and oil coolers have aluminum connectors (sometimes called bosses) joined to the outside by brazing using flux, etc., and these connectors are heat exchangers. It becomes a joint (adapter) between the pipe and the pipe.
The connector is an important part connecting the pipe and the heat exchanger, and high material strength is required from the reliability of the joining unit. For this reason, JIS A 3004 series Al—Mn—Mg alloy, JIS A 7000 series Al—Mg—Zn alloy and the like are often used for the member. Furthermore, since the connector is joined to the pipe by screwing the connector itself, the cutting ability as a material for screw machining and the screw strength at the time of joining the pipe after brazing are particularly required. Is done.

JP 2001-49374 A

Here, the screw strength refers to the torque strength at which the screw breaks when screwed to the pipe. In general, an appropriate hardness is required to improve the machinability of the material, and if it is too soft or too hard, the machinability decreases. On the other hand, the screw strength after brazing becomes more advantageous as the hardness is higher. If the hardness is below a certain value, the screw will rise when the screw is tightened. In conventional 3004 and 7000 series alloy boss materials, it is difficult to satisfy both of the above characteristics. When the thread cutting performance of the material is improved, the screw strength after brazing decreases, and the screw strength after brazing is reduced. If improved, there is a problem that the screw machinability of the material is lowered.
In addition, although general 7000 series alloys have high screw strength after brazing, they contain a large amount of Mg, which is highly effective in improving the strength, so that the flux (KAlF3, etc.) for removing the oxide film reacts with Mg in the material. By forming the compound, the brazing property of the connector is significantly lowered, and there is a problem that the brazing joint between the heat exchanger body and the connector material becomes weak. Moreover, since the addition of a large amount of Mg significantly improves the material hardness before brazing, there is a problem that the machinability for screw machining is greatly reduced.
Further, the material of Patent Document 1 has a problem that the amount of Mn that contributes to strength improvement and the amount of Mg that contributes to age hardening is not sufficient, and it takes time to obtain a desired strength after brazing. Connector materials are often fastened to pipes and screws quickly after brazing and need to improve strength in a short time.

  The present invention has been made against the background of the above circumstances, and has excellent brazing properties, high strength, high workability aluminum alloy material for brazing excellent in workability, and connector excellent in screw strength using the alloy material. One of the purposes is to provide materials.

  That is, among the high-strength processed aluminum alloy materials for brazing according to the present invention, the first present invention is mass%, Mn: 0.50-1.30%, Mg: 0.30-0.60% Zn: 4.5 to 6.5%, Fe: 0.10 to 0.30%, the balance is made of Al and inevitable impurities, Vickers hardness before brazing is 70 to 110, 600 Vickers hardness after 100 hours at room temperature after brazing heat treatment at 0 ° C. is 70 or more.

  The high-strength workable aluminum alloy material for brazing according to the second aspect of the present invention is the same as that of the first aspect of the present invention. .. 20% of which is characterized by containing one or two of them.

The high-strength aluminum alloy material for brazing of the third aspect of the present invention is the MgZn ₂ second phase having an equivalent circle diameter of 0.001 to 0.05 μm before brazing in the first or second aspect of the present invention. It is characterized in that particles are present at 1.0 × 10 ^{2 to} 1.0 × 10 ⁵ particles / mm ² .

The high-strength processed aluminum alloy material for brazing according to the fourth aspect of the present invention is the above-described first to third aspect of the present invention, having an equivalent circle diameter of 0.01 to 0.10 μm after 100 hours at room temperature after brazing. MgZn ₂ second phase particles are present in 1.0 × 10 ^{1 to} 1.0 × 10 ³ particles / mm ² .

  The connector material having excellent screw strength according to the fourth aspect of the present invention is characterized by comprising the high-strength aluminum alloy material for brazing.

  Below, the conditions prescribed | regulated by this invention are demonstrated. In the following description, all components are shown in mass%.

Mn: 0.50 to 1.30%
Mn has improved screw strength due to solid solution strengthening and dispersion hardening of intermetallic compounds. However, if the Mn content is less than 0.50%, sufficient strength cannot be obtained. On the other hand, when Mn is contained excessively, machinability is reduced. For this reason, Mn content is defined to the said range. For the same reason, it is desirable that the lower limit is 0.70% and the upper limit is 1.10%.

Mg: 0.30-0.60%
Mg forms second-phase particles such as Zn and MgZn ₂ to obtain age hardening and improve screw strength. However, when the Mg content is less than 0.30%, sufficient strength cannot be obtained. On the other hand, when Mg is contained excessively, brazing property is lowered. For this reason, Mg content is defined to the said range. For the same reason, it is desirable that the lower limit is 0.35% and the upper limit is 0.45%.

Zn: 4.5-6.5%
Zn is age-hardened by forming second phase particles such as Mg and MgZn ₂ and the screw strength is improved. However, if the Zn content is less than 4.5%, sufficient strength cannot be obtained. On the other hand, when Zn is contained excessively, the corrosion resistance is lowered, the melting point is lowered, and the brazing property is lowered. For this reason, Zn content is defined to the said range. For the same reason, it is desirable to set the lower limit to 5.0% and the upper limit to 6.0%.

Fe: 0.10 to 0.30%
Fe has improved screw strength by solid solution hardening or dispersion hardening of intermetallic compounds. However, if the Fe content is less than 0.10%, sufficient strength cannot be obtained. On the other hand, when Fe is contained excessively, machinability and corrosion resistance are lowered. For this reason, Fe content is defined to the said range. For the same reason, it is desirable that the lower limit is 0.15% and the upper limit is 0.25%.

Ti: 0.01-0.20%
Ti has improved screw strength due to solid solution strengthening and dispersion hardening of intermetallic compounds. However, if the Ti content is less than 0.01%, sufficient strength cannot be obtained. On the other hand, when Ti is contained excessively, castability, rollability, etc. will fall and manufacturability will deteriorate. For this reason, Ti content is defined to the said range. For the same reason, it is desirable to set the lower limit to 0.05% and the upper limit to 0.15%. In addition, Ti may be contained as an inevitable impurity at less than 0.005%.

Bi: 0.01-0.20%
Bi is added to improve brazing properties. However, the desired effect cannot be obtained when the Bi content is less than 0.01%. On the other hand, when Bi is contained excessively, castability, rollability, etc. will fall and manufacturability will deteriorate. For this reason, Bi content is defined to the said range. For the same reason, it is desirable to set the lower limit to 0.05% and the upper limit to 0.15%. In addition, Bi may be contained as an inevitable impurity at less than 0.005%.

Prior to brazing, the second phase particles of MgZn _{2 having} an equivalent circle diameter of 0.001 to 0.05 μm are 1.0 × 10 ^{2 to} 1.0 × 10 ⁵ particles / mm ^2.
The material strength changes depending on the dispersion state of the MgZn ₂ second phase particles, which affects the machinability before brazing. That is, if it is less than the lower limit of the range, the strength is inferior in machinability, and if it exceeds the upper limit, the improvement in strength is too great and the desired machinability cannot be obtained.

After 100 hours at room temperature after brazing, MgZn ₂ second phase particles having an equivalent circle diameter of 0.01 to 0.10 μm are 1.0 × 10 ^{1 to} 1.0 × 10 ³ particles / mm ^2.
The material strength varies depending on the dispersion state of the MgZn ₂ second phase particles, and affects the screw strength characteristics after brazing. That is, if it is less than the lower limit of the range, the strength is insufficient and the screw strength is inferior, and if it exceeds the upper limit, the particle size and the dispersion state are not appropriate, and the material strength is lowered and the desired screw strength cannot be obtained.

  As described above, according to the present invention, it is excellent in workability and brazing property, high strength is obtained after brazing, and can be suitably used as a connector material.

It is a figure which shows the connector periphery in one Embodiment of this invention.

Hereinafter, an embodiment of the present invention will be described.
The aluminum alloy of the present invention is by mass, Mn: 0.50 to 1.30%, Mg: 0.30 to 0.60%, Zn: 4.5 to 6.5%, Fe: 0.10 It contains 0.30%, and optionally contains Ti: 0.01-0.20%, Bi: 0.01-2.20%, one or two of them, the balance being Al and inevitable impurities The composition is made of In the present invention, the method for melting the aluminum alloy is not particularly limited, and a conventional method can be used.

The method for producing the aluminum alloy of the present invention is not particularly limited, but an extruded material is usually used because a connector material can be obtained without a special molding process by using a mold having a predetermined shape. The
Extrusion conditions usually extrude a billet that has been homogenized at 400 to 600 ° C into a predetermined shape at 400 to 600 ° C, but the extrusion conditions are not limited.

The aluminum alloy of the present invention can be used as a connector material 1 as shown in FIG. 1, and at that time, processing such as cutting is performed. In this embodiment, a screw hole 2 and a piping passage 3 are formed in the connector material 1.
The aluminum alloy of the present invention is subjected to brazing, but has a Vickers hardness of 70 to 110 before brazing. With this hardness, processing such as cutting can be performed satisfactorily.

The brazing conditions are not particularly limited, although the oxygen concentration is usually 100 ppm or less in an inert atmosphere such as nitrogen gas and the heat treatment is performed at 580 to 620 ° C. for about 1 to 5 minutes. The flux application amount is usually ^{2 to} 10 g / m ^2, but is not particularly limited.

After the connector material 1 is brazed to the heat exchanger body 10, the screw 22 is screwed into the screw hole through the flange 21 of the piping member 20, and the heat exchanger body 10 and the piping member 20 are joined.
It can have good strength after brazing. Assuming brazing heat treatment at 600 ° C. (the effect of brazing time is small and the difference is negligible), the Vickers hardness after 100 hours at room temperature is 70 or more.
When the Vickers hardness is 70 or more, it has high screw strength. If the screw strength is low, a screw will be raised at the time of tightening the screw, resulting in poor bonding, resulting in NG due to the soundness of the joint (no leakage, etc.). Since the connector material 1 is mounted on a vehicle or the like and receives vibrations or the like, it must be sufficiently screwed. The tightening torque of the M6 pitch screw is preferably 15 N · m or more, and the Vickers hardness exhibits sufficient strength against the tightening torque.

Influence of temperature and time in aging treatment In the aging treatment after hot working (preferably extrusion), it is necessary to control the precipitation of MgZn ₂ by optimizing the temperature and time. In general, precipitation proceeds for a long time when the temperature is low, and for a short time when the temperature is high.
In particular, the influence of the aging temperature is large. When the temperature is low, such as 100 ° C. or lower, precipitation is insufficient, and the MgZn ₂ second phase particles having an equivalent circle diameter of 0.001 to 0.05 μm are 1.0% before brazing. × 10 ² pieces / mm ² or more cannot be satisfied.
On the other hand, when the temperature is a high temperature of 220 ° C. or higher, the precipitation is promoted and the precipitate is coarsened, so that the MgZn ₂ second phase particles having an equivalent circle diameter of 0.001 to 0.05 μm are 1. 0 × 10 ⁵ pieces / mm ² or less cannot be satisfied.
Prior to brazing by optimizing the temperature conditions, the second phase particles of MgZn _{2 having} an equivalent circle diameter of 0.001 to 0.05 μm are 1.0 × 10 ^{2 to} 1.0 × 10 ⁵ particles / mm ^2. Therefore, the Vickers hardness after 70 hours at room temperature after brazing heat treatment at 600 ° C. satisfies 70 or more.

(Manufacturing method)
An aluminum alloy having the composition shown in Table 1 (remainder Al + inevitable impurities) was melted and cast by a DC method (semi-continuous casting method) to produce an 8-inch diameter billet. The billet cooling rate was 0.5 to 3.5 ° C./second. Furthermore, the obtained billet was subjected to a homogenization treatment at 500 ° C. for 4 hours, and then extruded at 500 ° C. to produce a 50 mm diameter round bar.
Furthermore, each aging process shown in Table 1 was implemented to the obtained round bar, and it was set as the test material.

(Brazing process)
The temperature was raised from room temperature to 600 ° C. at an average rate of temperature increase of 30 ° C./min, held at 600 ° C. for 3 minutes, and then subjected to brazing equivalent heating under the conditions of heat treatment for cooling at a rate of 100 ° C./min. The following evaluation tests were performed on the specimens after heating.

(Compound distribution state)
The number density (particles / μm ² ) of the second phase particles (dispersed particles) before and after brazing was measured with a transmission electron microscope (TEM). Before brazing, the material is subjected to salt bath annealing at 400 ° C for 15 seconds to remove deformation strain and make it easy to observe the compound. Then, a thin film is prepared by mechanical polishing and electrolytic polishing by ordinary methods. Each photograph was taken at 30000 times with a transmission electron microscope. Photographs were taken for each of the five fields of view, and the size and number density of the dispersed particles were measured by image analysis.

(Vickers hardness)
Based on JISZ2244, the Vickers hardness before and after brazing was measured.

(Corrosion test)
After 100 hours at room temperature after brazing, a salt spray test (SST) was carried out for 4 weeks (28 days). Corrosion weight loss after the test is less than 50mg / dm ² ◎, less than 50 or more ~100mg / mm ² ○, was evaluated as × 100 g / mm ² or more.

DESCRIPTION OF SYMBOLS 1 Connector material 2 Screw hole 10 Heat exchanger main body 20 Piping member 22 Screw

Claims (5)

  In mass%, Mn: 0.50 to 1.30%, Mg: 0.30 to 0.60%, Zn: 4.5 to 6.5%, Fe: 0.10 to 0.30% The balance consists of Al and inevitable impurities, the Vickers hardness before brazing is 70 to 110, and the Vickers hardness after 100 hours at room temperature after brazing heat treatment at 600 ° C. is 70 or more. High-strength processed aluminum alloy material for brazing.   The brazing according to claim 1, further comprising one or two of Ti: 0.01 to 0.20% and Bi: 0.01 to 0.20% by mass%. High-strength processed aluminum alloy material. _3. The MgZn ₂ second phase particles having an equivalent circle diameter of 0.001 to 0.05 μm are present at 1 × 10 ² to 1 × 10 ⁵ particles / mm ² before brazing. High-strength processed aluminum alloy material for brazing. The MgZn ₂ second phase particles having an equivalent circle diameter of 0.01 to 0.10 μm are present at 1.0 × 10 ^{1 to} 1.0 × 10 ³ particles / mm ² after 100 hours at room temperature after brazing. The high-strength processed aluminum alloy material for brazing according to any one of claims 1 to 3.   A connector material excellent in screw strength, comprising the high-strength processed aluminum alloy material for brazing according to any one of claims 1 to 4.

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