Patent Application
20140225042
The present invention relates to a flexible conductive material and a cable using the same, used for, for example, a lead wire particularly subject to be bent repeatedly in an area of wiring industrial robots, commercial robots, and automobiles.
When a metal material, especially, a conductive wire made mainly of copper or aluminum is used for wiring an industrial robot, a commercial robot, or an automobile, the conductive wire is subject to a cyclic bending load while driving an arm or opening and closing a door. In light of this, instead of the normal conductive wire, the conductive wire resistant to the cyclic bending load is used. In addition, the conductive wire with a small diameter is more resistant to the cyclic bending load, so that a stranded cable formed of a plurality of thin wires is used rather than a solid wire.
As an example of conductive materials, for example, Patent Literature 1 discloses an aluminum alloy wire rod consisting of an aluminum alloy containing the following elements: 0.1-0.4 mass % iron, 0.1-0.3 mass % copper, 0.02-0.2 mass % magnesium, 0.02-0.2 mass % silicon, and 0.001-0.01 mass % of a combination of titanium and vanadium. The aluminum alloy wire rod has a crystal grain size of 5-25 μm in a vertical section in a wire drawing direction. A fatigue life of the aluminum alloy wire rod is 50,000 times or more provided that the aluminum alloy wire rod is subjected to a cyclic fatigue of ±0.15% strain oscillation at normal temperature.
Patent Literature 1: Japanese Unexamined Patent Application Publication No. 2010-163675
In the technique disclosed in Patent Literature 1, the fatigue life is 50,000 times or more. However, an actual robot moves 86,400 times in two days if one motion of the robot takes two seconds. For this reason, the technique disclosed in Patent Literature 1 is not sufficient. In light of this, the inventors of the present invention achieved the present invention through their earnest studies on factors affecting the fatigue life on condition that the conductive material is resistant to one million times or more of dynamic driving tests.
The present invention has been made in view of the above circumstances, and it is an object of the present invention to provide a flexible conductive material and a cable using the same, which are resistant to one million times or more of dynamic driving (e.g., cyclic bending) and particularly suitable for wiring robots or automobiles.
To accomplish the above object, a first aspect of the present invention provides a flexible conductive material, comprising crystal grains forming a metal texture of a base material, an average crystal grain size of the crystal grains being 2 μm or less, the flexible conductive material further characterized by being resistant to one million times or more of dynamic driving tests.
As a method of setting the average crystal grain size of the crystal grains forming the metal texture of the base material 2 μm or less, the following methods can be taken: (1) a processing method such as a supercool rolling (including drawing) and a differential speed rolling; (2) a miniaturizing method, in which an alternating current and a direct current magnetic field are applied to a solidifying metal (a metal under being solidified) and thereby electromagnetic oscillations are given to the solidifying metal; (3) a method of rapid rate sintering (e.g., plasma discharge sintering, etc.) metal powders crushed to be 2 μm or less in average; (4) a method of sintering metal powders; and (5) a method of combining a process (e.g., a rotary forging work using a swaging machine) and a heat treatment.
By setting the average crystal grain size of the crystal grains forming the metal texture of the base material 2 μm or less, a lot of crystal grains can exist in the metal texture of the base material. Accordingly, when the generated cracks grow, the cracks can frequently come into collision with the crystal grains. By this, each growth direction of the cracks is changed. At the same time, divarications of the cracks are promoted, thereby reducing a growth rate of the cracks and improving a flexibility of the metal texture of the base material.
To accomplish the above object, a second aspect of the present invention provides a flexible conductive material, comprising crystal grains forming a metal texture of a base material, an average crystal grain size of the crystal grains being 2 μm or less, at least 20% or more of the crystal grains in a cross sectional ratio being 1 μm or less, the flexible conductive material further characterized by being resistant to one million times or more of dynamic driving tests.
By setting the average crystal grain size of the crystal grains forming the metal texture of the base material 2 μm or less, a lot of crystal grains can exist in the metal texture of the base material. Accordingly, when the generated cracks grow, the cracks can frequently come into collision with the crystal grains. By this, each of the growth directions of the cracks is changed. At the same time, the divarications of the cracks are promoted, thereby reducing the growth rate of the cracks and improving the flexibility of the metal texture of the base material. Furthermore, by performing a texture control to set the 1-μm or less crystal grains at least 20% or more in the cross sectional ratio, the number of the crystal grains in the metal texture of the base material can be further increased. As a result, when the generated cracks grow, the cracks can notably come into collision with the crystal grains, and the changes in the growth directions of the cracks and the divarications of the cracks occur frequently.
In the flexible conductive material according to the first and the second aspects of the present invention, it is preferable that the flexible conductive material includes 0.1 mass % to 20 mass % of nanoparticles. The crack stops every time when the crack comes into collision with the nanoparticle, thus the growth rate of the crack can be decreased. Here, if the contained amount of the nanoparticles is less than 0.1 mass %, the number of the nanoparticles is decreased and the crack less frequently comes into collision with the nanoparticle, thereby the crack does not stop notably. On the other hand, if the contained amount of the nanoparticles exceeds 20 mass %, a lot of the nanoparticles exist in the grain boundaries and the strength of the conductive material is decreased, which is not preferable.
In the flexible conductive material according to the first and the second aspects of the present invention, it is possible that the flexible conductive material includes 0.1 mass % to 20 mass % of spherical nanoparticles. The spherical nanoparticles can prevent a particular stress concentrated part from being generated around the nanoparticles.
Now, the nanoparticle is referred to as a particle having a grain size in a range from 1 nm to 999 nm.
In addition, the nanoparticles exist in the grain boundaries of the particles forming the main metal texture of the conductive material, inside the particles, or in the grain boundaries and inside the particles. To disperse the nanoparticles in the grain boundaries, inside the particles, or in the grain boundaries and inside the particles, the following methods can be taken: (1) a method of dissolving the nanoparticles in a metal and precipitating the nanoparticles inside the particles or in the grain boundaries when the metal is solidified; (2) a method of mixing the nanoparticles with a dissolved metal in advance, solidifying the metal while stirring (e.g., magnetic stirring), and forcibly dispersing the nanoparticles in the grain boundaries; (3) a method of rapid sintering a mixed powders in which the nanoparticles are dispersed uniformly in metal powders of 2 μm or less in average, and allowing the nanoparticles to exist between the metal powders (grain boundaries); and (4) a method of adding an element forming a compound with a metal to the dissolved metal and precipitating the nanoparticles inside the particles, in the grain boundaries, and inside the particles and in the grain boundaries as nanosized compounds when the metal is solidified.
In the flexible conductive material according to the first and the second aspects of the present invention, the base material is made of any of copper, aluminium, and magnesium.
In the flexible conductive material according to the first and the second aspects of the present invention, the nanoparticles are any one of fullerenes, silicon nanoparticles, transition metal nanoparticles, compound nanoparticles consisting of compounds with the base material, oxide nanoparticles consisting of oxides of the base material, and nitride nanoparticles consisting of nitrides of the base material.
To accomplish the above object, a third aspect of the present invention provides a cable characterized by using the flexible conductive material according to the first and the second aspects of the present invention.
Since the flexible conductive material according to the first and the second aspects of the present invention is resistant to one million times or more of the dynamic driving tests, the flexible conductive material is applicable to electric wires or cables used for purposes subject to a cyclic load such as a cyclic bending (e.g., robots or automobiles). As a result, breaking of the wires or cables in use can be prevented, thereby improving reliability of devices and reducing burdens in maintenances of the devices.
If the flexible conductive material according to the first and the second aspects of the present invention includes 0.1 mass % to 20 mass % of the nanoparticles, when the cracks generated due to the cyclic load passing along the grain boundaries, tips of the cracks are pinned by the nanoparticles to stop the growth of the cracks or to decrease the growth rate of the cracks. Thus, a period for the conductive material to be broken (a life of the conductive material) is prolonged (i.e., a flexibility of the conductive material is improved). In addition, in a case of the spherical nanoparticles, a particular stress concentrated part can be prevented from being generated around the nanoparticle. Thus, the period for the conductive material to be broken can be further prolonged (i.e., the flexibility of the conductive material is further improved).
In the flexible conductive material according to the first and the second aspects of the present invention, if the base material is made of copper or aluminium, an electrical conductivity of the conductive material can be improved. This makes it possible to provide lead wires and cables with good electrical conductivities.
In addition, if the base material is made of magnesium, the electrical conductivity is inferior to copper and aluminium but the material can be lightened drastically. As a result, it is possible to manufacture superiorly flexible and lightweight lead wires and cables.
In the flexible conductive material according to the first and the second aspects of the present invention, if the nanoparticles are any one of fullerenes, silicon nanoparticles, transition metal nanoparticles, compound nanoparticles consisting of compounds of the base material, oxide nanoparticles consisting of oxides of the base material, and nitride nanoparticles consisting of nitrides of the base material, the optimal nanoparticles can be dispersed in accordance with characteristics and purposes.
Since the cable according to the third aspect of the present invention uses the flexible conductive material according to the first and the second aspects of the present invention, the cable with a superior flexibility can be manufactured. This can prevent the cable from being cut off while the cable is in use, improving reliability of devices and reducing burdens in maintenances of the devices.
Referring to the accompanying drawings, embodiments of the present invention will be described.
A cable according to a first embodiment of the present invention is formed by a flexible conductive material resistant to one million times or more of cable flex tests (an example of dynamic driving tests). As shown in
While the cable flex test is conducted, if a crack is generated on a surface of the wire 10 (to which the maximum cyclic bending stress is loaded), the crack grows mainly along a grain boundary 12 between the crystal grains 11 forming the wire 10. Thus, every time when the crack growing along the grain boundary 12 comes into collision with the crystal grain 11, a growing direction of the crack is changed. When a crack moves in a certain direction by a certain distance from one point in the surface of the wire 10, an average crack growth rate (e.g., an average crack growth rate of a crack when the crack passes across the surface of the wire 10 from one point to another opposing point on the surface of the wire 10) becomes superficially slow. Furthermore, if the crack comes into collision with the crystal grain 11 and diverges from the crystal grain 11, a crack growth energy working on a tip of the crack is decreased and thereby the growth rate of the crack is decreased.
In light of this, when the crystal grains 11 forming the main metal texture of the conductive material of the wire 10 has an average crystal grain size of 2 μm or less, a collision of the crack with the crystal grains 11 can stimulate the change in the crack growth direction and the divarication of the crack while a strength of the wire 10 (base material) is maintained. As a result, if the crack is generated on the wire 10, a length of time until the wire 10 is split by the crack becomes long and the number of cycles to fracture of the cable in the cable flex tests is increased.
Now, it is preferable that the average crystal grain size of the crystal grains 11 is 2 μm or less as well as a texture control is taken in a way that at least 20% or more in a cross sectional ratio of the 1-μm or less crystal grains 11 are included. By this, the collision of the crack with the crystal grains 11 can be caused remarkably, which allows frequent occurrences of the growth direction change of the crack and the divarication of the crack. As a result, the number of cycles to fracture of the cable in the cable flex tests is further increased.
As shown in
A cable according to a second embodiment of the present invention is formed by a conductive material resistant to one million times or more of cable flex tests. As shown in
The crack of the wire 19 generated in the cable flex test grows mainly along the grain boundary 21 between the crystal grains 20 forming the wire 19. If the nanoparticle 22 exists on the grain boundary 21, the crack growing along grain boundary 21 comes into collision with the nanoparticle 22. The growth of the crack stops every time when the crack comes into collision with the nanoparticle 22. In order to make a further growth of the crack collided with the nanoparticle 22, it is necessary for the crack to detour the nanoparticle 22 (i.e., to move along a boundary between the nanoparticle 22 and the crystal grain 20) and to reach the grain boundary 21 again. Therefore, if the nanoparticles 22 exist on the grain boundaries 21, an average crack growth rate of the cracks moving in a certain direction by a certain distance from one point on the surface of the wire 19 (e.g., an average crack growth rate of the cracks moving across the wire 19 from one point on one surface of the wire 19 to an opposing point on the other surface of the wire 19) becomes very slow superficially. As a result, if the crack is generated on the wire 19, a length of time until the wire 19 is split by the crack becomes long, and the number of cycles to fracture of the cable is further increased in the cable flex tests.
Now, if the nanoparticle 22 has a spherical shape, a particular stress concentrated part can be prevented from being generated around the nanoparticle 22 and thus the crack can certainly grow along the surface of the nanoparticle 22. By this, a length of time until the conductive material is broken can be further prolonged (i.e., a flex resistance of the conductive material is improved).
In addition, a contained amount of the nanoparticles 22 is 0.1 mass % to 20 mass %. Also, the nanoparticle 22 is any one of the followings: fullerene; silicon nanoparticle; transition metal nanoparticle (e.g., metallic nanoparticle such as gold, silver, copper, and iron); compound nanoparticle consisting of compound of the base material (e.g., intermetallic compound); oxide nanoparticle consisting of oxide of the base material (e.g., if the base material is aluminum, nanoparticle of Al2O3 is added); and nitride nanoparticle consisting of nitride of the base material (e.g., if the base material is aluminum, nanoparticle of MN is added). Furthermore, a carbon nanotube can be used as the nanoparticle.
As shown in
Also, as shown in
Hereinafter, a description will be given on experimental examples for confirming functional effects of the present invention.
A formulation containing 0.6 mass % of magnesium, 0.3 mass % of silicon, 0.05 mass % of iron and further containing, as a rest part, aluminum and unavoidable impure substances was dissolved. After that, a solution treatment was performed at 520° C. and an aging treatment was performed at 175° C. for eight hours, thereby an aluminum system conductive material block was produced. Next, from the conductive material block, four wire rods of 10 mm diameter were produced by a cutting work. Using a swaging machine, a rotary forging work was performed to process the wire rods into a wire rod of 5 mm diameter (one rod), wire rods of 2 mm diameter (two rods), and a wire rod of 1.5 mm diameter (one rod). Each of the processed wire rods were heat treated in a heat treat furnace. At the moment, a recrystallization temperature of the wire rod was calculated in advance using a thermal decomposition device (pyrolytic equipment). The heat treatments of each of the wire rods were performed for 2-40 hours in argon atmosphere at a temperature lower than the calculated recrystallization temperature by 50° C. After the heat treatments, each of the naturally-cooled wire rods were cold-worked and processed into drawn wire materials of 80 μm diameter through a die wire drawing work.
Texture observations of the drawn wire materials found out the followings: an average crystal grain size of crystal grains forming a metal texture was 1 μm in a case where the wire rod of the 1.5 mm diameter was heat-treated for two hours; an average crystal grain size of crystal grains forming a metal texture was 2 μm in a case where the wire rod of the 2 mm diameter was heat-treated for eight hours; an average crystal grain size of crystal grains forming a metal texture was 3 μm in a case where the wire rod of the 2 mm diameter was heat-treated for 16 hours; and an average crystal grain size of crystal grains forming a metal texture was 8 μm in a case where the wire rod of the 5 mm diameter was heat-treated for 40 hours. In addition, each of the drawn wire materials having the average crystal grain size of 1 μm, 2 μm, or 3 μm contained 50%, 20%, and 20% in a cross sectional ratio of the 1-μm or less crystal grains, respectively. The drawn wire material having the average crystal grain size of 8 μm contained 0% in a cross sectional ratio of the 1-μm or less crystal grains. Furthermore, in each of the drawn wire materials, 0.3 mass % of β double prime habit having a grain size of 10-100 nm existed as a nanoparticle.
Then, conductivities of the obtained drawn wire materials were measured. Also, using the drawn wire materials as wires, a cable having a cross section of 0.2 mm2 was manufactured and this cable was used as a specimen. In a way that the cable was subject to a 100-g load, cable flex tests were conducted by cyclically bending the cable side to side with a bending radius of 15 mm and a bending angle being in a range of ±90 degrees. Table 1 shows the conductivities and the results of the cable flex tests.
The conductivity of each of the drawn wire materials was 53% IACS. Also, the number of breakages in the cable flex tests was as follows: one million and twenty thousand (1,200,000) times in Experimental Example 1 (when the average crystal grain size was 2 μm, the cross sectional ratio of the 1-μm or less crystal grains was 20%, and the contained amount of the nanoparticles was 0.3 mass %); and 85 thousand (850,000) times in Experimental Example 3 (when the average crystal grain size was 3 μm, the cross sectional ratio of the 1-μm or less crystal grains was 20%, and the contained amount of the nanoparticles was 0.3 mass %). In short, when the average crystal grain size of the crystal grains of the drawn wire material was 2 μm or less, the cable was resistant to one million times or more of the cable flex tests. Furthermore, in Experimental Example 4 (when the average crystal grain size was 1 μm, the cross sectional ratio of the 1-μm or less crystal grains was 50%, and the contained amount of the nanoparticles was 0.3 mass %), the number of breakages in the cable flex tests was five million times. Thus, as the average crystal grain size becomes smaller and the rate of the contained amount of the 1-μm or less crystal grains becomes higher, the number of breakages in the cable flex tests increased more.
A formulation containing 0.6 mass % of magnesium, 0.3 mass % of silicon, 0.05 mass % of iron and further containing, as a rest part, aluminum and unavoidable impure substances was dissolved. After that, a solution treatment was performed at 520° C., thereby an aluminum system conductive material block (hereinafter referred to as Block 0) was produced. Also, a solution treatment was performed at 520° C. and an aging treatment was performed at 175° C. for one hour and for eight hours respectively, thereby aluminum system conductive material blocks (hereinafter referred to as Block 1 and Block 8, respectively) were produced. Next, respectively from Block 0 and Block 8, wire rods of 10 mm diameter were produced by a cutting work. Using a swaging machine, a rotary forging work was performed to process the wire rods into wire materials with 5 mm diameter. In a similar way, from Block 1, a wire rod of 10 mm diameter was produced and processed into a wire material with 2 mm diameter using the swaging machine. From Block 8, a wire rod of 10 mm diameter was produced and processed into a wire material with 1.5 mm diameter using the swaging machine. Each of the processed wire rods was heat treated in a heat treat furnace. At the moment, a recrystallization temperature of the wire rod was calculated in advance using a thermal decomposition device. The heat treatments of each of the wire rods were performed in argon atmosphere for 12 hours at a temperature lower than the calculated recrystallization temperature by 50° C. After the heat treatments, each of the naturally-cooled wire rods was cold-worked and processed into drawn wire materials of 80 μm diameter through a die wire drawing work.
Texture observations of the drawn wire materials found that an average crystal grain size of crystal grains forming a metal texture was 2 μm. Also, the rate (the cross sectional ratio) of the 1-μm or less crystal grains in each of the drawn wire materials was as follows: 0% when the rotary forging work was performed to process the wire rod into the wire material with 5 mm diameter using the swaging machine; 20% when the rotary forging work was performed to process the wire rod into the wire material with 2 mm diameter using the swaging machine; and 50% when the rotary forging work was performed to process the wire rod into the wire material with 1.5 mm diameter using the swaging machine. Furthermore, in each of the drawn wire materials, β double prime habit having a grain size of 10-80 nm existed as a nanoparticle. The contained amounts of the β double prime habit were 0.05 mass % when the aging treatment was performed at 175° C. for one hour and 0.3 mass % when the aging treatment was performed at 175° C. for eight hours. In addition, the drawn wire material made of Block 0, which have not undertook the aging treatment at 175° C., did not include the β double prime habit.
Then, conductivities of the obtained drawn wire materials were measured. Also, using the drawn wire materials as wires, a cable having a cross section of 0.2 mm2 was manufactured and the cable flex tests as the same as Experimental Examples 1-4 were conducted. Table 1 shows the conductivities and the results of the cable flex tests.
The conductivity of each of the drawn wire materials was as follows: 54% IACS when the contained amount of the nanoparticles was 0.05 mass %; and 53% IACS when the contained amount of the nanoparticles was 0.3 mass % or 0%. Also, the number of breakages in the cable flex tests was as follows: one million and ten thousand (1,100,000) times in Experimental Example 5 (when the average crystal grain size was 2 μm, the cross sectional ratio of the 1-μm or less crystal grains was 0%, and the contained amount of the nanoparticles was 0.3 mass %); and one million and thirty thousand (1,300,000) times in Experimental Example 6 (when the average crystal grain size was 2 μm, the cross sectional ratio of the 1-μm or less crystal grains was 50%, and the contained amount of the nanoparticles was 0.3 mass %). In short, when the ratio of the 1-μm or less crystal grains included in the metal texture was increased, the number of breakages in the cable flex tests was also increased. Furthermore, in Experimental Example 7 (when the average crystal grain size was 2 μm, the cross sectional ratio of the 1-μm or less crystal grains was 0%, and the contained amount of the nanoparticles was 0 mass %), the number of breakages in the cable flex tests was one million times. Thus, when 0.3 mass % of the nanoparticles was included in the metal texture, the number of breakages in the cable flex tests was increased.
7 mass % gold particles and 20 mass % gold particles with 200-nm or less diameters were added respectively to aluminum powders with 99.9% purity (100 mesh), and then a mechanical alloying treatment was performed (in which an acceleration of gravity was 20 G and a period was 7,200 seconds). Next, using a spark plasma sintering machine, each of the mechanical alloyed powders was heated at 500° C. for 600 seconds under a pressurized condition of 41 MPa, thereby manufacturing rods of solidified molded materials each having a diameter of 10 mm. After that, using a swaging machine, each of the solidified molded materials with 10-mm diameter was processed into a wire material with 2-mm diameter by a rotary forging work, and each of the obtained wire materials was heat treated in a heat treat furnace. At the moment, a recrystallization temperature of the solidified molded material was calculated in advance using a thermal decomposition device. The heat treatments of each of the solidified molded materials were performed for 12 hours in argon atmosphere at a temperature lower than the calculated recrystallization temperature by 50° C. After the heat treatments, each of the naturally-cooled wire materials were cold-worked and processed into drawn wire materials of 80 μm diameter through a die wire drawing work.
Texture observations of the drawn wire materials found that an average crystal grain size of crystal grains forming a metal texture was 2 μm. Also, the rate (the cross sectional ratio) of the 1-μm or less crystal grains in each of the drawn wire materials was 20%.
Then, conductivities of the obtained drawn wire materials were measured. Also, using the drawn wire materials as wires, a cable having a cross section of 0.2 mm2 was manufactured and the cable flex tests as the same as Experimental Examples 1-4 were conducted. Table 1 shows the conductivities and the results of the cable flex tests.
The conductivity of each of the drawn wire materials was as follows: 40% IACS when the contained amount of the nanoparticles was 7 mass %; and 45% IACS when the contained amount of the nanoparticles was 20 mass %. Also, the number of breakages in the cable flex tests increased with a higher rate of the contained amount of the nanoparticles.
0.3 mass % gold particles with 200-nm or less diameters were added to copper powders with 99.9% purity (100 mesh), and then a mechanical alloying treatment was performed (in which an acceleration of gravity was 20 G and a period was 7,200 seconds). After that, using a spark plasma sintering machine, the powders were heated at 500° C. for 600 seconds under a pressurized condition of 41 MPa, thereby manufacturing rods of solidified molded materials P each having a diameter of 10 mm. In addition, the identical mechanical alloying treatment was performed only for the copper powders (the copper powders were crushed while being given an impact). Using the spark plasma sintering machine, the mechanical alloyed copper powders were heated in the same heating condition as described above, thereby manufacturing rods of solidified molded materials Q each having a diameter of 10 mm. Next, using a swaging machine, the solidified molded materials P were processed into wire materials with 2-mm diameter and with 5-mm diameter respectively by a rotary forging work, whereas the solidified molded materials Q were processed into wire materials with 5-mm diameter by the rotary forging work. Then, each of the obtained wire materials was heat treated in a heat treat furnace. At the moment, each recrystallization temperature of the solidified molded materials P and Q was calculated in advance using a thermal decomposition device. In argon atmosphere at a temperature lower than the calculated recrystallization temperature by 50° C., the solidified molded materials P were heat treated for four hours and for eighty hours respectively, and the solidified molded materials Q were heat treated for four hours. After the heat treatments, each of the naturally-cooled wire materials was cold-worked and processed into drawn wire materials of 80 μm diameter through a die wire drawing work.
Texture observations of the drawn wire materials found out the followings: when the solidified molded materials P were processed into the wire materials with 2-mm diameters by the rotary forging work using the swaging machine and then heat treated for four hours, an average crystal grain size of crystal grains forming a metal texture was 2 μm and a rate (cross sectional ratio) of 1-μm or less crystal grains was 20%; when the solidified molded materials P were processed into the wire materials with 5-mm diameters by the rotary forging work using the swaging machine and then heat treated for eighty hours, the average crystal grain size of the crystal grains forming the metal texture was 8 μm and the rate (cross sectional ratio) of the 1-μm or less crystal grains was 0%; and further when the solidified molded materials Q were processed into the wire materials with 5-mm diameters by the rotary forging work using the swaging machine and then heat treated for four hours, the average crystal grain size of the crystal grains forming the metal texture was 2 μm and the rate (cross sectional ratio) of the 1-μm or less crystal grains was 0%.
Conductivities of the obtained drawn wire materials were measured. Also, using the drawn wire materials as wires, a cable having a cross section of 0.2 mm2 was manufactured and the cable flex tests as the same as Experimental Examples 1-4 were conducted. Table 1 shows the conductivities and the results of the cable flex tests.
The conductivity of the drawn wire materials made of the solidified molded materials Q was 100% IACS, whereas the conductivities of the drawn wire materials made of the solidified molded materials P and having the average crystal grain size of 2 μm and 8 μm were both 70% IACS. Also, the number of breakages in the cable flex tests was as follows: eight hundred thousand (800,000) times when the average crystal grain size was 8 μm; and more than one million times when the average crystal grain size was 2 μm.
0.3 mass % gold particles with 200-nm or less diameters were added to magnesium powders with 99.9% purity (100 mesh), and then a mechanical alloying treatment was performed (in which an acceleration of gravity was 20 G and a period was 7,200 seconds). After that, using a spark plasma sintering machine, the powders were heated at 500° C. for 600 seconds under a pressurized condition of 41 MPa, thereby manufacturing rods of solidified molded materials R each having a diameter of 10 mm. In addition, the identical mechanical alloying treatment was performed only for the magnesium powders (the magnesium powders were crushed while being given an impact). Using the spark plasma sintering machine, the mechanical alloyed magnesium powders were heated in the same heating condition as described above, thereby manufacturing rods of solidified molded materials S each having a diameter of 10 mm. Next, using a swaging machine, the solidified molded materials R were processed into wire materials with 2-mm diameters and with 5-mm diameters respectively by a rotary forging work, whereas the solidified molded materials S were processed into wire materials with 5-mm diameters by the rotary forging work. Then, each of the obtained wire materials was heat treated in a heat treat furnace. At the moment, each recrystallization temperature of the solidified molded materials R and S was calculated in advance using a thermal decomposition device. In argon atmosphere at a temperature lower than the calculated recrystallization temperature by 50° C., the solidified molded materials R were heat treated for three hours and for sixty hours respectively, and the solidified molded materials S were heat treated for three hours. After the heat treatments, each of the naturally-cooled wire materials were cold-worked and processed into drawn wire materials of 80 μm diameter through a die wire drawing work.
Texture observations of the drawn wire materials found out the followings: when the solidified molded materials R were processed into the wire materials with 2-mm diameters by the rotary forging work using the swaging machine and then heat treated for three hours, an average crystal grain size of crystal grains forming a metal texture was 2 μm and a rate (cross sectional ratio) of 1-μm or less crystal grains was 20%; when the solidified molded materials R were processed into the wire materials with 5-mm diameters by the rotary forging work using the swaging machine and then heat treated for sixty hours, the average crystal grain size of the crystal grains forming the metal texture was 8 μm and the rate (cross sectional ratio) of the 1-μm or less crystal grains was 0%; and further when the solidified molded materials S were processed into the wire materials with 5-mm diameters by the rotary forging work using the swaging machine and then heat treated for three hours, the average crystal grain size of the crystal grains forming the metal texture was 2 μm and the rate (cross sectional ratio) of the 1-μm or less crystal grains was 0%.
Conductivities of the obtained drawn wire materials were measured. Also, using the drawn wire materials as wires, a cable having a cross section of 0.2 mm2 was manufactured and the cable flex tests as the same as Experimental Examples 1-4 were conducted. Table 1 shows the conductivities and the results of the cable flex tests.
The conductivity of the drawn wire materials made of the solidified molded materials S was 38% IACS, whereas the conductivities of the drawn wire materials made of the solidified molded materials R and having the average crystal grain size of 2 μm and 8 μm were both 30% IACS. Also, the number of breakages in the cable flex tests was as follows: fifty thousand (50,000) times when the average crystal grain size was 8 μm; and more than one million times when the average crystal grain size was 2 μm.
The present invention is not limited to the above-described embodiments, but can include modifications within a scope of the present invention.
The flexible conductive material and the cable using the same according to the present invention are resistant to one million times or more of the dynamic driving tests. Thus, the conductive material and the cable using the same according to the present invention are suitable for purposes subject to cyclic bending, for example, electric wires and cables used for devices such as robots and automobiles including driving members, thereby improving reliability of the devices and reducing burdens in maintenances of the devices. As a result, operation rates of the devices can be improved and running costs of the devices can be cut down.
10: wire, 11: crystal grain, 12: grain boundary, 16: wire, 17: coarse crystal grain, 18: grain boundary, 19: wire, 20: crystal grain, 21: grain boundary, 22: nanoparticle, 23: wire, 24: crystal grain, 25: nanoparticle, 26: grain boundary, 27: wire, 28: crystal grain, 29: nanoparticle, 30: grain boundary
| Number | Date | Country | Kind |
|---|---|---|---|
| 2011-146305 | Jun 2011 | JP | national |
| Filing Document | Filing Date | Country | Kind | 371c Date |
|---|---|---|---|---|
| PCT/JP2012/066412 | 6/27/2012 | WO | 00 | 12/18/2013 |
