JP7650827B2 - Fastening materials - Google Patents

Description

The present invention relates to a fastening member.

Traditionally, one approach to improving the fuel efficiency of automobiles has been to reduce the weight of various parts. For example, aluminum alloys have been used instead of cast iron as the material for engine blocks, and magnesium alloys have been used instead of steel as the material for engine covers and oil pans.

As part of the weight reduction mentioned above, there has been a growing trend to use aluminum alloys and magnesium alloys as materials for fastening members that fasten parts together. In particular, aluminum alloy bolts have a small difference in linear expansion coefficient with the aluminum and magnesium alloys that make up various parts, and are less susceptible to galvanic corrosion. This makes them ideal for weight reduction, as they ensure fastening reliability even when the screw holes in parts are made shallow and the bolt diameter is made narrower.

The aluminum alloys used for fastening members are 6000 series aluminum alloys, which are suitable for strength, heat resistance, corrosion resistance, and workability. In order to further improve the properties, adjustments to the components and the use of 7000 series aluminum alloys, which have higher strength than the 6000 series, are being considered (see, for example, Patent Documents 1 and 2). In Patent Document 1, the properties are improved by including a specified amount of strontium (Sr).

JP 2013-104123 A JP 2017-202497 A

However, conventional aluminum alloys had the problem of low resistance to loosening due to stress relaxation (relaxation resistance).

The present invention has been made in consideration of the above, and aims to provide a fastening member that has excellent relaxation resistance.

In order to solve the above-mentioned problems and achieve the object, the fastening member of the present invention is characterized in that it contains, by mass, 0.6% or more and 1.4% or less of silicon, 0.5% or more and 5.0% or less of copper, 0.3% or more and 1.1% or less of manganese, 0.5% or more and 1.3% or less of magnesium, and 0.01% or more and 0.8% or less of zinc, with the remainder being aluminum and unavoidable impurities, and has a circular equivalent average crystal grain size in the region from the surface to a depth of 200 μm of 4 μm or more and 50 μm or less.

In addition, the fastening member of the present invention is characterized in that, in the above invention, the average crystal orientation difference in the region from the surface to a depth of 200 μm is 1.5 degrees or less.

In addition, the fastening member of the present invention is characterized in that, in the above invention, the ratio of the proportional limit to the tensile strength is 0.6 or more.

According to the present invention, a fastening member having excellent relaxation resistance can be provided.

FIG. 1 is a side view showing the configuration of a fastening member according to a first embodiment of the present invention. FIG. 2 is a flowchart illustrating the method for manufacturing the fastening member according to the first embodiment of the present invention. FIG. 3 is a plan view showing the configuration of a fastening member according to the second embodiment of the present invention. FIG. 4 is a diagram showing a crystal grain map in the thread root of the fastening member according to Example 1 of the present invention. FIG. 5 is a diagram showing a crystal grain map in the thread root of a fastening member according to Example 2 of the present invention. FIG. 6 is a diagram showing a crystal grain map in the thread root of a fastening member according to Example 3 of the present invention. FIG. 7 is a diagram showing a crystal grain map in the thread root of a fastening member according to Example 4 of the present invention. FIG. 8 is a diagram showing a crystal grain map in the thread root of the fastening member according to Comparative Example 1 of the present invention. FIG. 9 is a diagram showing a crystal grain map in the thread root of a fastening member according to Comparative Example 2 of the present invention. FIG. 10 is a diagram showing a crystal grain map in the thread root of a fastening member according to Comparative Example 3 of the present invention. FIG. 11 is a diagram showing a crystal grain map in the thread root of a fastening member according to Comparative Example 4 of the present invention. FIG. 12 is a diagram showing a crystal orientation difference map in the thread groove of the fastening member according to Example 1 of the present invention. FIG. 13 is a diagram showing a crystal orientation difference map in the thread groove of the fastening member according to Example 2 of the present invention. FIG. 14 is a diagram showing a crystal orientation difference map in the thread groove of the fastening member according to Comparative Example 1 of the present invention. FIG. 15 is a diagram showing a crystal orientation difference map in the thread groove of a fastening member according to Comparative Example 2 of the present invention. FIG. 16 is a diagram for explaining the timing of measuring the axial force in the relaxation resistance test.

Hereinafter, a mode for carrying out the present invention (hereinafter referred to as "embodiment") will be described with reference to the attached drawings. Note that the drawings are schematic, and the relationship between the thickness and width of each part, the thickness ratio of each part, etc. may differ from the actual ones, and the drawings may include parts with different dimensional relationships and ratios.

(Embodiment 1)
FIG. 1 is a side view showing the configuration of a fastening member according to a first embodiment of the present invention. The fastening member 1 shown in FIG. 1 is a bolt (a type of male screw) made of an aluminum (Al) alloy. The fastening member 1 includes a cylindrical shaft portion 2, a head portion 3 provided at one end of the shaft portion 2 in the axial direction (left-right direction in FIG. 1), and a neck portion 4 forming a boundary between the shaft portion 2 and the head portion 3. The shaft portion 2 has a threaded portion 22 having a thread 21 formed on its surface. Note that the shape of the head portion 3 (hexagonal trim type) is merely an example, and other shapes (hexagonal flange type, pan type, dish type, truss type, flat type, etc.) may be used. Note that a thread groove 23 is formed between adjacent threads 21 in the axial direction of the shaft portion 2. The head portion 3 is not necessarily required, and a stud bolt without a head (for example, JIS standard: JIS B 1173) may be used.

The fastening member 1 is made of an aluminum alloy containing silicon (Si), copper (Cu), manganese (Mn), magnesium (Mg) and zinc (Zn), with the balance being aluminum (Al) and unavoidable impurities. The aluminum alloy according to this embodiment is an alloy having a composition equivalent to the aluminum alloy having the alloy number A6056, or an alloy having a composition equivalent to the aluminum alloy A6056 with an increased amount of Cu. Specifically, the aluminum alloy contains, by mass ratio, 0.6% to 1.4% Si, 0.5% to 5.0% Cu, 0.3% to 1.1% Mn, 0.5% to 1.3% Mg, and 0.01% to 0.8% Zn. The aluminum alloy may also contain a combination of zirconium (Zr) and titanium (Ti) at 0.2% or less. The Cu content (standard value) of the A6056 aluminum alloy is 0.5% to 1.1%. In the following description, the content refers to the content ratio in mass ratio.In the following description, the content refers to the content ratio in mass ratio.

In the aluminum alloy according to the first embodiment, Si precipitates as _Mg2Si by aging treatment, and the precipitation of _Mg2Si can increase the strength. If the Si content exceeds 1.4%, the elongation of the alloy is reduced. If the Si content is less than 0.6%, the strength improving effect of the _Mg2Si precipitates is insufficient.

Cu precipitates _CuAl2 and _Al2CuMg by aging treatment, and these precipitates can increase the strength. In particular, if the Cu content is 1.5% or more and 4.0% or less, the amount of these precipitates can be further increased, and the strength can be further improved. On the other hand, if the Cu content exceeds 5.0%, the corrosion resistance, stress corrosion cracking resistance, and elongation of the alloy are reduced. Also, if the Cu content is less than 0.5%, the strength improvement effect of these precipitates is insufficient.

Mn is an element that exhibits solid solution strengthening. In addition, aging treatment also produces Al-Mn-Si precipitates, which can increase strength. Here, if the Mn content exceeds 1.1%, the elongation of the alloy decreases. Furthermore, if the Mn content is less than 0.3%, the strength-improving effect of these precipitates is insufficient.

Mg can increase strength by precipitating _Mg2Si during aging treatment. If the Mg content exceeds 1.3%, elongation is reduced. If the Mg content is less than 0.5%, the strength improving effect of the _Mg2Si precipitates is insufficient.

Zn increases strength by precipitating _MgZn2 during aging treatment. If the Zn content exceeds 0.8%, the corrosion resistance, stress corrosion cracking resistance, and elongation of the alloy are reduced. If the Zn content is less than 0.01%, the strength improvement effect of these precipitates is insufficient.

The fastening member 1 has a circular average grain size of 4 μm or more and 50 μm or less in the region from the surface of the thread groove 23 to a depth of 200 μm. Here, the depth from the thread groove 23 is the distance from the surface of the thread groove 23 toward the central axis of the shaft portion 2 and perpendicular to this central axis. The circular average grain size here is the diameter of the circle. If the circular average grain size is less than 4 μm, grain boundary sliding is likely to occur, which is thought to reduce the relaxation resistance. On the other hand, if the circular average grain size exceeds 50 μm, ductility is reduced and the possibility of cracks occurring during the heading process or rolling process increases.

In addition, the fastening member 1 has a KAM (Kernel Average Misorientation) value, which indicates the average crystal orientation difference in the region from the surface of the thread valley 23 to a depth of 200 μm, of 1.5 degrees or less. If the KAM value exceeds 1.5 degrees, there is a lot of residual strain, which is thought to reduce relaxation resistance.

In addition, the fastening member 1 has a tensile strength of 400 MPa or more. If the tensile strength is less than 400 MPa, the fastening member will need to be enlarged in order to maintain the load resistance (reduced axial force resistance) during fastening, which will impair weight reduction.

Furthermore, the fastening member 1 has a 0.2% yield strength, which is the stress at which the permanent strain remaining after unloading is 0.2%, of 370 MPa or more. If the 0.2% yield strength is less than 370 MPa, the load when fastening in the elastic region is small, and compensating for this requires the fastening member to be made larger, which compromises the weight reduction.

Furthermore, the ratio of the proportional limit to the tensile strength of the fastening member 1 (proportional limit/tensile strength) is 0.6 or more, and preferably 0.7 or more. If the ratio (proportional limit/tensile strength) is less than 0.6, the load when fastening in the elastic region is relatively small, and compensating for this requires an increase in the size of the fastening member, thereby compromising the weight reduction. The proportional limit is the maximum stress at which Hooke's law holds true on the stress-strain curve.

The fastening member 1 is formed by processing a rod-shaped member made of the above-mentioned aluminum alloy. Figure 2 is a flowchart explaining a method for manufacturing the fastening member according to the first embodiment of the present invention.

First, the rod-shaped member described above is pressed (step S101). In this pressing process, the rod-shaped member is clamped between dies and pressurized. By pressing, for example, one end of the rod-shaped member is crushed to produce a first molded product having a shaft portion 2, a head portion 3, and a neck portion 4 excluding a threaded portion 22.

Then, the first molded product formed by pressing is rolled (step S102). In this rolling process, the first molded product is sandwiched between dies with projections and recesses corresponding to the threads and pressurized. While rotating the first molded product, one die is moved relative to the other die to form the threads 21 on the shaft portion 2. A threaded portion 22 is formed on the shaft portion 2 by the rolling process.

After the rolling process, the second molded product having the threaded portion 22 formed therein is subjected to a heat treatment (step S103). In the heat treatment, the second molded product is treated at a high temperature to be solutionized (solution treatment), and then subjected to an aging treatment. The set temperature for the solution treatment is preferably set to 500°C to 570°C, and the set temperature for the aging treatment is preferably set to 140°C to 200°C.

By manufacturing the fastening member 1 according to the above-mentioned process, it is possible to obtain the fastening member 1 having the above-mentioned characteristics. Conventionally, it is common to carry out the heat treatment in step S103 before the rolling process in step S102.

According to the embodiment 1 of the present invention described above, a fastening member having excellent relaxation resistance can be obtained by manufacturing a fastening member 1 using an aluminum alloy containing, by mass, 0.6% to 1.4% silicon, 0.5% to 5.0% copper, 0.3% to 1.1% manganese, 0.5% to 1.3% magnesium, and 0.01% to 0.8% zinc, with the remainder being aluminum and unavoidable impurities, and by performing a rolling process and then a heat treatment.

(Embodiment 2)
Fig. 3 is a plan view showing the configuration of a fastening member according to a second embodiment of the present invention. The fastening member 5 shown in Fig. 3 is a nut (a type of female thread) made of the above-mentioned aluminum alloy. The fastening member 5 has a hollow cylindrical shape, and a screw thread 52 is formed on the inner surface of a hole 51 formed in the center. Note that the shape of the fastening member 5 shown in Fig. 3 (hexagonal nut) is merely one example, and it is also possible to realize it as a nut having another shape (flange nut, cap nut, high nut, etc.).

The fastening member 5 is formed of the above-mentioned aluminum alloy and has a ring shape. The fastening member 5 is manufactured in the same manner as in embodiment 1 for a rod-shaped member made of the above-mentioned aluminum alloy. For example, after rolling the thread 52, heat treatment is performed.

According to the second embodiment of the present invention described above, a fastening member 5 is manufactured using an aluminum alloy containing, by mass, 0.6% to 1.4% silicon, 0.5% to 5.0% copper, 0.3% to 1.1% manganese, 0.5% to 1.3% magnesium, and 0.01% to 0.8% zinc, with the remainder being aluminum and unavoidable impurities, and is subjected to a rolling process and then a heat treatment, thereby obtaining a fastening member with excellent relaxation resistance.

Although the embodiments for carrying out the present invention have been described above, the present invention should not be limited to the above-mentioned embodiments 1 and 2. For example, the fastening member according to the present invention can be realized as a machine screw or a tapping screw, which is a male screw other than a bolt.

Below, we will explain examples of the aluminum alloy according to the present invention. Note that the present invention is not limited to these examples.

Example 1
A bolt (corresponding to the fastening member 1) was produced by rolling and then heat-treating a rod-shaped member of A6056 aluminum alloy according to the flow chart shown in FIG. 2. The bolt produced in this example has a thread size of M8 and a pitch of 1.25. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread valley using the electron backscatter diffraction (EBSD) method for a part of this bolt. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The average grain size and average crystal orientation difference are values in the region from the bolt surface to depths of 100, 200, and 400 μm. The results are shown in Table 1.

Example 2
A bolt was produced by processing a rod-shaped member having a Cu content of 2.04% in the composition of A6056 aluminum alloy according to the flow chart shown in Figure 2. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread groove by EBSD method for a part of this bolt. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

Example 3
A rod-shaped member having an A6056 aluminum alloy composition with a Si content of 0.92%, an Fe content of 0.24, a Cu content of 2.90%, an Mn content of 0.65%, an Mg content of 0.89%, and a Zr+Ti content of 0.17% was used to prepare a bolt by processing according to the flow chart shown in FIG. 2. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread groove by the EBSD method for a part of this bolt. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

Example 4
A rod-shaped member having an A6056 aluminum alloy composition with a Si content of 0.92%, a Cu content of 3.94%, a Mn content of 0.69%, a Mg content of 0.88%, and a Zr+Ti content of 0.17% was used to prepare a bolt by processing according to the flow chart shown in FIG. 2. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread groove by the EBSD method for a part of this bolt. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

(Comparative Example 1)
A bolt was produced by using a rod-shaped member of A6056 aluminum alloy and performing the rolling process in step S102 and the heat treatment in step S103 in the flow chart shown in Figure 2 in a reversed order. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread groove by EBSD for some of the bolts. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

(Comparative Example 2)
A bolt was produced by using a rod-shaped member having a Cu content of 2.04% in the composition of A6056 aluminum alloy, and by processing the rolling process in step S102 and the heat treatment in step S103 in the flow chart shown in Figure 2 in a reversed order. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread groove by the EBSD method for some of the bolts. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

(Comparative Example 3)
A rod-shaped member having a composition of A6056 aluminum alloy with a Si content of 0.92%, a Fe content of 0.24, a Cu content of 2.90%, a Mn content of 0.65%, a Mg content of 0.89%, and a Zr+Ti content of 0.17% was used, and a bolt was produced by switching the processing order of the rolling process in step S102 and the heat treatment in step S103 in the flow chart shown in FIG. 2. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread valley by the EBSD method for some of the bolts. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

(Comparative Example 4)
A rod-shaped member having a composition of A6056 aluminum alloy with a Si content of 0.92%, a Cu content of 3.94%, a Mn content of 0.69%, a Mg content of 0.88%, and a Zr+Ti content of 0.17% was used, and a bolt was produced by switching the order of the rolling process in step S102 and the heat treatment in step S103 in the flow chart shown in FIG. 2. The average grain size and average crystal orientation difference (KAM value) were obtained for each depth of the thread valley by the EBSD method for some of the bolts. In addition, a tensile test was performed on the bolt to obtain the tensile strength, 0.2% proof stress, and proportional limit/tensile strength. The results are shown in Table 1.

[Average crystal grain size]
FIG. 4 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Example 1 of the present invention. FIG. 5 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Example 2 of the present invention. FIG. 6 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Example 3 of the present invention. FIG. 7 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Example 4 of the present invention. FIG. 8 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Comparative Example 1 of the present invention. FIG. 9 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Comparative Example 2 of the present invention. FIG. 10 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Comparative Example 3 of the present invention. FIG. 11 is a diagram showing a crystal grain map in the thread valley of the fastening member according to Comparative Example 4 of the present invention. FIGS. 4 to 11 correspond to a part of a cross section including the deepest part of the thread valley (corresponding to the thread valley 23) of the bolt produced. The boundary line (black line) shown in the figure indicates a grain boundary with an orientation difference of 5° or more, and the grain surrounded by this boundary line is considered to be one crystal grain. The color shades in the figures are given according to the orientation in which the crystal grains are oriented. In Examples 1 to 4 and Comparative Examples 1 to 4, the average grain size is the distance from the deepest part of the thread valley (e.g., position P ₀ shown in FIG. 4 ), and the average grain size in each region from the surface to 100 μm, 200 μm, and 400 μm away from the center axis of the bolt shaft (corresponding to shaft 2) in the direction perpendicular to the center axis was calculated. As can be seen from the results shown in Table 1 and from FIGS. 4 to 11 , at each depth, the average grain size of the bolts (Examples 1 to 4) manufactured by rolling and heat treatment is larger than the average grain size of the bolts (Comparative Examples 1 to 4) manufactured by heat treatment and rolling. Also, when Example 1 is compared with Examples 2 to 4, it can be seen that the composition with more Cu has a larger average grain size.

[Average crystal orientation difference]
FIG. 12 is a diagram showing a crystal orientation difference map in the thread valley of the fastening member according to Example 1 of the present invention. FIG. 13 is a diagram showing a crystal orientation difference map in the thread valley of the fastening member according to Example 2 of the present invention. FIG. 14 is a diagram showing a crystal orientation difference map in the thread valley of the fastening member according to Comparative Example 1 of the present invention. FIG. 15 is a diagram showing a crystal orientation difference map in the thread valley of the fastening member according to Comparative Example 2 of the present invention. FIGS. 12 to 15 correspond to a part of a cross section including the deepest part of the thread valley (corresponding to the thread valley 23) of the manufactured bolt. The average crystal orientation difference (KAM value) was calculated as the average of the orientation differences between all measurement points adjacent to the measurement point with a diameter of about 0.7 μm in each region from the surface to a depth of 100 μm, 200 μm, and 400 μm. As can be seen from the results shown in Table 1 and from FIGS. 12 to 15, at each depth, the average crystal orientation difference of the bolts produced by rolling and heat treatment (Examples 1 and 2) is smaller than the average crystal orientation difference of the bolts produced by heat treatment and rolling (Comparative Examples 1 and 2).

[Tensile strength, 0.2% yield strength, and proportional limit/tensile strength]
The tensile strength and 0.2% proof stress shown in Table 1 are the average values obtained by measuring 10 times. The minimum and maximum values are shown in parentheses in the lower row. The proportional limit is the stress (load) when the relationship between the load and the stroke deviates from a straight line. If the proportional limit/tensile strength is 0.6 or more, the load during fastening in the elastic region can be relatively increased, making it possible to reduce the size of the fastening member, which in turn promotes weight reduction of the fastening member.

[Relaxation resistance]
The bolt was fastened to the workpiece at room temperature, heated at 120°C for 20 hours, and then cooled to room temperature, and the axial force after heating was measured. FIG. 16 is a diagram for explaining the measurement timing of the axial force in the relaxation resistance test. In FIG. 16, the time change of the axial force is shown by a solid line F ₁ , and the time change of the temperature is shown by a broken line T _1. The temperature t ₀ is room temperature. In the relaxation resistance test, the axial force before heating (point Q ₁ ) and the axial force after heating (point Q ₂ ) were compared. It can be said that the smaller the change between the axial force before heating (point Q ₁ ) and the axial force after heating (point Q ₂ ) is, the more relaxation resistance there is. The axial force before heating was set to 12.5 kN, which corresponds to the plastic region fastening of the A6056 aluminum alloy under these fastening conditions. The axial forces after heating of the bolts according to Examples 1 and 2 were 9.0 kN and 9.8 kN, whereas the axial forces after heating of the bolts according to Comparative Examples 1 and 2 were 8.2 kN and 8.8 kN. From these results, it can be seen that the bolts subjected to heat treatment after rolling, as in Examples 1 and 2, have better relaxation resistance.

In this way, the present invention can include various embodiments not described here, and various design changes can be made without departing from the technical idea specified by the claims.

As described above, the fastening member of the present invention is suitable for obtaining a fastening member having excellent relaxation resistance.

Reference Signs List 1, 5 Fastening member 2 Shank 3 Head 4 Neck 21, 52 Thread 22 Threaded portion 23 Thread root 51 Hole

Claims (5)

The alloy contains, by mass ratio, 0.6% to 1.4% silicon, more than 1.1% to 5.0% copper, 0.3% to 1.1% manganese, 0.5% to 1.3% magnesium, and 0.01% to 0.8% zinc, with the balance being aluminum and unavoidable impurities;
The circle-equivalent average crystal grain size in the region from the surface to a depth of 200 μm is 4 μm or more and 50 μm or less.
A fastening member characterized by: The average crystal orientation difference in the region from the surface to a depth of 200 μm is 1.5 degrees or less.
The fastening member according to claim 1 . The ratio of the proportional limit to the tensile strength is 0.6 or more.
The fastening member according to claim 1 or 2. Contains 1.5% or more and 4.0% or less of copper by mass ratio;
The fastening member according to claim 1 . The circle-equivalent average crystal grain size in the region from the surface to a depth of 200 μm is 9 μm or more and 50 μm or less;
The fastening member according to claim 4 .

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