WO2009119237A1 - ベリリウム銅鍛造バルク体 - Google Patents

ベリリウム銅鍛造バルク体 Download PDF

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Publication number
WO2009119237A1
WO2009119237A1 PCT/JP2009/053449 JP2009053449W WO2009119237A1 WO 2009119237 A1 WO2009119237 A1 WO 2009119237A1 JP 2009053449 W JP2009053449 W JP 2009053449W WO 2009119237 A1 WO2009119237 A1 WO 2009119237A1
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Prior art keywords
forged
copper
beryllium
bulk body
hardness
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PCT/JP2009/053449
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English (en)
French (fr)
Japanese (ja)
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尚国 村松
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日本碍子株式会社
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Application filed by 日本碍子株式会社 filed Critical 日本碍子株式会社
Priority to CN200980111010.XA priority Critical patent/CN101981211B/zh
Priority to JP2010505469A priority patent/JP5416091B2/ja
Priority to EP09725472.6A priority patent/EP2264199B1/en
Publication of WO2009119237A1 publication Critical patent/WO2009119237A1/ja
Priority to US12/880,429 priority patent/US20100329923A1/en

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    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C22C9/06—Alloys based on copper with nickel or cobalt as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C9/00—Alloys based on copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
    • C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
    • C22F1/08—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of copper or alloys based thereon

Definitions

  • the present invention relates to a beryllium copper forged bulk body.
  • Beryllium copper bulk material is used for machine structural parts that require durability and reliability, such as aircraft bearings, submarine cable repeater casings, ship rotor shafts, oilfield drilling collars, injection molds, Used for welding electrode holders. In general, these applications require the machinability and high hardness or strength of the bulk material.
  • Beryllium copper is a precipitation-hardening type copper alloy like many high-strength copper alloys, and its bulk material is well known to those skilled in the art: casting-homogenization annealing-hot working-solution annealing (solution treatment)- Manufactured after underwater quench-age hardening.
  • Patent Document 1 shows that by carefully selecting each processing condition, crystal grains are refined to some extent, and strength and fatigue life, which are important for mechanical structural parts, can be improved.
  • Patent Document 2 shows that crystal grains can be refined to an unprecedented level by diligently examining the forging method and the processing conditions during forging.
  • the cause of this phenomenon is the value that indicates hardness as the dimensional distance of the bulk material advances from the end toward the inside, as explained in JIS G4052 (structural steel with guaranteed hardenability). Is also estimated from the remarkable decrease.
  • the phenomenon that the hardness value decreases from the surface to the inside is a common issue not only for steel materials but also for copper alloy bulk materials prepared through rapid quenching in water after heat treatment. The larger it was, the more noticeable it was. Patent No. 2827102 JP 2005-096442 A
  • an object of the present invention is to provide a forged beryllium-copper bulk body that can maintain uniform hardness from the surface to the inside, has high reliability, is excellent in fatigue life, and is less prone to processing strain. .
  • a forged beryllium copper bulk body containing at least Be and Cu, the hardness of the central portion is 0 to 10% harder than the hardness of the surface, and the Vickers hardness of the central portion is Provided is a forged beryllium-copper bulk product having a tensile strength of 240 N or more, a tensile strength of 800 N / mm 2 or more, and uniformity so that variations in measured values of tensile strength in any direction are within 5%. Is done.
  • a forged beryllium-copper bulk body that can maintain uniform hardness from the surface to the inside, has high reliability, has excellent fatigue life, and is less prone to processing strain.
  • FIG. 3 (a) is a graph showing the relationship between the treatment time and the temperature when the solution treatment and the overaging treatment of FIG. 2 are discontinuously performed
  • FIG. 3 (b) shows the solution treatment and It is a graph which shows the relationship between the processing time at the time of implementing an overaging process continuously, and temperature. It is a table
  • surface which shows the relationship between the amount of rolling and distortion amount which concerns on one Embodiment of this invention.
  • FIG. 5A is an external view of a forged beryllium-copper bulk body according to an embodiment of the present invention
  • FIG. 5B is a pressure applied during repeated pressurization when the reduction amount is 18%.
  • FIG. 5C shows the change in surface temperature immediately after repeated pressurization.
  • FIG. 6 (a) is an external view of a conventional forged beryllium copper bulk body
  • FIG. 6 (b) shows the relationship between the applied pressure and the cumulative strain amount during repeated pressing when the reduction amount is 33%.
  • FIG. 6C shows the change in surface temperature immediately after repeated pressurization.
  • FIG. 7A is a perspective view showing a test piece for measuring the hardness of a beryllium copper forged bulk body
  • FIG. 7B is a cold forging process for the beryllium bulk body according to an embodiment of the present invention.
  • FIG. 7 (c) is a graph showing the relationship between the distance from the side end surface immediately after to the center direction and the Vickers hardness
  • FIG. 7C shows the direction from the side end surface after age hardening of the beryllium bulk body according to an embodiment of the present invention to the center direction. It is a graph which shows the relationship between distance and Vickers hardness. It is a graph which shows the relationship between the distance from the side end surface of the conventional forged beryllium-copper bulk body to a center direction, and Vickers hardness.
  • a forged beryllium-copper bulk body 1 is an alloy containing beryllium (Be) and copper (Cu), and has three axial directions (Z in FIG. 1) orthogonal to each other. It is a rectangular parallelepiped alloy having sides a, b, and L extending along the axis, the X axis, and the Y axis.
  • the ratio of the lengths of the sides a, b, and L of the forged beryllium copper bulk body 1 is not particularly limited.
  • the size of the forged beryllium copper bulk body 1 is not particularly limited. However, if the dimensions of the sides a, b, and L are too large, it becomes difficult to control the manufacturing conditions, which will be described later, due to the influence of processing heat generated from the beryllium copper forged bulk body 1 during forging. Therefore, as the dimensions of the forged beryllium copper bulk body 1, for example, a, b, and L can be in the range of about 50 to 500 mm, preferably 80 to 400 mm.
  • Forged beryllium copper bulk body 1 is (1) Cu 100- (a + b) Be a Co b (0.4% ⁇ a ⁇ 2.0%, 0.15% ⁇ b ⁇ 2.8%, a + b ⁇ 3.5%) Or (2) Cu 100- (a + b) Be a Co b (0.4% ⁇ a ⁇ 2.0%, 0.15% ⁇ b ⁇ 2.8%, a + b ⁇ 3.5%) It is preferable that Fe, S, and P to be limited can be limited to less than 0.01% by weight.
  • the reason why the weight ratio of Be is set to 0.4% or more is to improve the strength by the precipitated phase composed of Be and Cu and / or Be and Co.
  • the reason why the weight ratio of Be is set to 2.0% or less is to improve the strength by suppressing the coarsening of the precipitated phase composed of Be and Co.
  • the reason why the weight ratio of Co is set to 0.15% or more is to improve the strength by adding Co.
  • the reason why the weight ratio of Co is 2.8% or less is to suppress the coarsening of the precipitated phase composed of Be and Co.
  • the reason why the weight ratio of the forged beryllium-copper bulk body 1 is the combination of (2) is to reduce the weight ratio of Be by adding Ni cheaper than Be in order to reduce the cost of the material.
  • the reason why the weight ratio of Be is set to 0.05% or more is to improve the strength by the precipitated phase composed of Be and Ni.
  • the reason why the weight ratio of Be is set to 0.6% or less is to obtain a sufficient cost reduction effect by reducing the weight ratio of Be.
  • the reason why the weight ratio of Ni is set to 1.0% or more is to improve the strength by adding Ni.
  • the reason why the weight ratio of Ni is 2.4% or less is to suppress a decrease in electrical conductivity and an increase in melting point due to Ni contained in the Cu matrix.
  • Fe, S, and P which are impurities, are limited to less than 0.01% by weight, is that when these elements are contained in an amount of 0.01% or more, segregation at the grain boundaries is likely to occur. This is because the product easily breaks.
  • the forged beryllium-copper bulk body 1 in FIG. 1 has a fine granular structure (average particle diameter ⁇ 2 ⁇ m) and has a precipitated phase containing at least Be precipitated from Cu.
  • the “average particle diameter” refers to an average particle diameter measured by the following measurement method.
  • A Crystal orientation analysis is performed using SEM / EBSP (Scanning Electron Microscope / Electron Back Scatter Diffraction Pattern) method, and a grain size distribution is obtained by counting boundaries where orientation difference ⁇ is greater than 2 ° as grain boundaries.
  • B Confirm that the average misorientation ⁇ of all counts is 15 ° or more.
  • C Calculate the average grain size from the crystal grain size distribution. Generally, the misorientation ⁇ is 0 ° ⁇ ⁇ ⁇ 4 °. A structure composed only of subcrystals with boundaries is not counted as a crystal grain.
  • the orientation difference ⁇ is composed only of subcrystals having a boundary of 0 ° ⁇ ⁇ ⁇ 4 °.
  • the organization is also considered to be a part of the entire organization at this moment. Therefore, a structure having an average orientation difference of 15 ° or more is counted as a crystal grain.
  • the forged beryllium-copper bulk body 1 is an alloy having the same hardness (or gradually hardens) from the end face toward the inner center, and the hardness of the central portion is 0 to 10% harder than the hardness of the surface.
  • the Vickers hardness (HV) of the surface (edge) is 218 to 450, more preferably 273 to 450, and the Vickers hardness of the inner center is 240 to 450, more preferably 300 to 450.
  • the “Vickers hardness” in the present embodiment is, for example, parallel to the XZ plane direction so as to include the center of the rectangular (cubic) beryllium copper forged bulk body 1 shown in FIG.
  • the cut-out flat plate 2 is used as a test piece, and an arbitrary point on the test piece is defined as JISZ2244 (Vickers hardness test-test method (corresponding international standard: ISO / 6507-1; The result measured according to is shown.
  • the forged beryllium-copper bulk body 1 is a polycrystalline body having no anisotropy in crystal orientation (random orientation) based on the hardness, structure, ultrasonic depth test, observation results of crystal grains by the EBSP method, and the like described later.
  • a tensile strength of 800 N / mm 2 or more preferably 800 ⁇ 1500N / mm 2, more preferably 1100 ⁇ 1500N / mm 2, even 1100 ⁇ 1300N / mm 2. If the tensile strength is less than 800 N / mm 2 , the mechanical strength and fatigue life are lowered, which may be inappropriate for the market for machine structural parts.
  • the value of the tensile strength of the forged beryllium bulk body 1 is isotropic (uniform) in any forging direction or in a direction that forms 45 ° with the forging direction in a plane including the forging direction.
  • the variation (measurement average value) in the measured value of the strength was within 5%.
  • the measuring method of tensile strength is as follows. First, a flat plate including the XY, YZ, and XZ planes is cut out from the center of the forged beryllium bulk body 1, and six directions (that is, X, Y, Z, X) representing arbitrary directions are cut out from the respective flat plates.
  • the tensile test piece was machined so that 45 ° between Y and 45 °, 45 ° between YZ and 45 ° between X and Z) coincided with the tensile axis. Although the test piece was produced in accordance with JISZ2201, a sample whose size was reduced to 1 ⁇ 2 due to the restriction of the size of the material was used. The produced test piece was measured according to JISZ2241 (metal material tensile test method).
  • the beryllium copper forged bulk body 1 is polycrystalline when it has anisotropy (particularly weak specific direction) in a direction deviated by specific angles ⁇ , ⁇ , ⁇ from the X, Y, Z directions.
  • an abnormal value should be recognized somewhere in the six directions.
  • the variation in the value of the tensile strength when measured in the above six directions is within 5%, and no abnormal value was measured. Therefore, it can be said that the forged beryllium-copper bulk body 1 according to the present embodiment has isotropic (uniformity) in tensile strength in any arbitrary direction, and the values are approximately the same. .
  • step S10 in FIG. 2 Be (or a Be compound) is dissolved in a Cu matrix to produce a copper alloy in which dislocations are not generated in crystal grains.
  • the weight ratio of Cu 100- (a + b) Be a Co b (0.4% ⁇ a ⁇ 2.0%, 0.15% ⁇ b ⁇ 2.8%, a + b ⁇ 3.5%), or Cu 100- ( c + d) Be c Ni d (0.05% ⁇ c ⁇ 0.6%, 1.0% ⁇ d ⁇ 2.4%, c + d ⁇ 3.0%) in a high frequency melting furnace Make a lump.
  • Fe, S, and P as impurities can be limited to less than 0.01% by weight.
  • the obtained ingot is heated and held for a predetermined holding time (1 hour to 24 hours) in a solid solution temperature range (in the range of 700 ° C. to 1000 ° C.), thereby generating non-equilibrium during casting. Remove and homogenize non-uniform structures that adversely affect subsequent processes such as segregation.
  • step S11 the copper alloy obtained in S10 is forged and processed into a rectangular parallelepiped copper alloy having a desired size.
  • the oxide film formed on the surface of the plate-like copper alloy is removed by cutting.
  • the copper alloy obtained in step S11 is heated for a predetermined solid solution holding time (1 hour to 24 hours) in the solid solution temperature range (in the range of 700 ° C. to 1000 ° C.).
  • the Be (or Be compound) is dissolved in the Cu matrix.
  • the copper alloy obtained in step S12 is held for a predetermined time (2 to 6 hours) in the overaging temperature range (within a range of 550 to 650 ° C.).
  • the precipitated particles of the copper alloy are reduced to a size (for example, an average particle size of about 1 ⁇ m) that does not adversely affect each manufacturing process after step S13.
  • the solution treatment of step S12 and the overaging process of step S13 may each be processed independently (discontinuous), as shown in FIG.3 (b). It may be processed continuously.
  • step S14 the copper alloy obtained in step S13 is cooled by water cooling, air cooling, or standing cooling so that the surface temperature of the copper alloy becomes, for example, 20 ° C. or less.
  • the cooling rate varies depending on the size of the bulk body, but is preferably ⁇ 100 ° C. s ⁇ 1 or more (preferably ⁇ 200 ° C. s ⁇ 1 or more).
  • the cooled copper alloy is forged while cooling and extracting heat. Forging is performed from the X-axis, Y-axis, and Z-axis directions of a rectangular parallelepiped that are orthogonal to each other. As for the order of forging, it is preferable to apply pressure sequentially from the axial direction corresponding to the longest side among the sides of the copper alloy.
  • step S151 pressure is applied from the Z-axis direction to the cooled copper alloy by a forging device or the like. It is preferable to keep the surface temperature of the copper alloy during the pressurization at 120 ° C. or less (more preferably within the range of 20 to 100 ° C.). When the surface temperature exceeds 120 ° C., a shear band structure that crosses a plurality of crystal grains is likely to be generated, so that cracks and breakage occur, and the shape before processing cannot be maintained.
  • the pressurizing pressure is preferably 1200 MPa or less. When the pressurization pressure exceeds 1200 MPa in combination with the overaging conditions, etc., there is a risk that cracks and breakage may occur because the copper alloy tends to form a shear band structure that crosses a plurality of crystal grains.
  • the reduction amount (working rate (%)) for one treatment in step S151 is in the range of 18 to 30%, and the amount of plastic strain (strain amount; ⁇ ) applied to the copper alloy is 0.2 to 0.00. It is preferable to be within the range of 36.
  • step S152 the copper alloy obtained in step S151 is cooled.
  • the cooling method may be any method such as air cooling, water cooling, and natural cooling, but considering the efficiency and efficiency of repetitive work, cooling by water cooling is desirable.
  • the cooling is preferably performed so that the surface temperature of the hot copper alloy generated from the copper alloy by pressurization is 20 ° C. or less.
  • step S153 pressure is applied from the Y-axis direction to the cooled copper alloy by a forging device or the like.
  • the surface temperature of the copper alloy during the pressurization is preferably maintained at 120 ° C. or lower.
  • the reduction amount (processing rate (%)) for one treatment in step S153 is in the range of 18 to 30%, and the amount of plastic strain (strain amount; ⁇ ) applied to the copper alloy is 0.2 to 0.00. It is preferable to be within the range of 36.
  • step S154 the copper alloy obtained in step S153 is cooled. Cooling is preferably performed so that the surface temperature of the copper alloy is 20 ° C. or lower.
  • step S155 pressure is applied from the X-axis direction to the cooled copper alloy by a forging device or the like.
  • the surface temperature of the copper alloy during the pressurization is preferably maintained at 120 ° C. or lower.
  • the reduction amount (working rate (%)) for one treatment in step S155 is in the range of 18 to 30%, and the amount of plastic strain (strain amount; ⁇ ) applied to the copper alloy is 0.2 to 0.00. It is preferable to be within the range of 36.
  • step S156 the copper alloy obtained in step S155 is cooled. Cooling is preferably performed so that the temperature of the copper alloy is 20 ° C. or lower.
  • step S157 the operator determines whether or not the number of pressurizations to the copper alloy by the forging device has reached a predetermined number.
  • the “number of times of pressurization” refers to the number of times counted up when a pressure is applied to the copper alloy from any one of the directions of each axis (X axis, Y axis, Z axis).
  • the “predetermined number of pressurizations” refers to the number of times that the cumulative value of plastic strain applied to the copper alloy (cumulative strain amount; ⁇ total) is, for example, 1.8 or more. If the number of pressurization times has not reached the predetermined pressurization number, the processes of steps S151 to S156 are repeated. If the number of pressurizations has reached the predetermined number of pressurizations, the process proceeds to step S16.
  • step S16 (age hardening treatment) the copper alloy obtained in step S15 is subjected to a predetermined age hardening time (1 to 24 hours) in the precipitation temperature range (200 ° C. to 550 ° C.).
  • the Be (or Be compound) contained in the copper alloy is precipitation-hardened by holding. Thereby, the beryllium copper forged bulk body shown in FIG. 1 can be manufactured.
  • the forged copper alloy in the cold forging process of step S15, is forged while being cooled and extracted so that the surface temperature of the copper alloy after cooling is maintained at 120 ° C. or lower.
  • the amount of plastic strain applied to the copper alloy can be increased while reducing the influence of processing heat generated by the copper alloy during forging, so it has uniform and fine crystal grains and is uniform from the surface to the inside. Forged beryllium-copper bulk material with a high hardness can be produced.
  • step S14 it may not be possible to cool uniformly from the surface to the center of the interior by simply performing the cooling treatment of step S14 after the solid solution process of step S12.
  • the cooling treatment of step S14 it was not possible to rapidly cool the interior center to the extent that the surface was cooled by water quenching or the like.
  • the cold forging process in step S15 is performed in a state where the inner center is not sufficiently cooled, the deformation of the product becomes non-uniform and breakage, cracks during processing, warpage, and the like are likely to occur.
  • the processing conditions are controlled so that the copper alloy after the solution treatment is dared to be slowly and inefficiently cooled in step S13 instead of being rapidly cooled as in the prior art. That is, in step S13, the copper alloy after the solution treatment is treated at an overaging temperature (550 to 650 ° C.) for a predetermined time (overaging time: 2 to 6 hours), whereby suitably precipitated particles are suitably obtained. The effect of working and deforming uniformly to the inside is obtained. This suppresses the generation of a shear band structure that crosses multiple crystal grains and prevents cracks and fractures, so that it can maintain uniform hardness from the surface to the inside, has excellent fatigue life, and has a processing strain. It has been found that a copper beryllium bulk body can be obtained which is less prone to cause the occurrence of copper.
  • the overaging temperature in step S13 is less than 550 ° C., it is difficult to grow the precipitated particles, and if it is higher than 650 ° C., Be dissolves in Cu, which is not preferable. If the overaging time is less than 2 hours, the precipitated particles do not grow to a certain size. Conversely, even if the time is longer than 6 hours, the growth of the precipitated particles has been completed to some extent, which is not efficient. Accordingly, the overaging temperature is preferably 550 to 650 ° C., more preferably 570 to 630 ° C., and the overaging treatment time is preferably 2 to 6 hours, more preferably 3 to 5 hours.
  • the number of pressurizations is increased by a predetermined amount in step S157. It is determined whether or not the number of times of pressure has been reached, but is not limited to this, and it is determined whether or not the number of pressurizations reaches a predetermined number of pressurizations each time pressure is applied to the copper alloy. May be.
  • each forging in each axial direction is completed once in the cooling step shown in steps S152, S154, S156.
  • the copper alloy is cooled.
  • the object can be achieved by forging while maintaining the surface temperature of the copper alloy to be processed at 120 ° C. or lower, and therefore the cooling steps shown in steps S152, S154, and S156 may be omitted as necessary.
  • a normal forging device is used as a method of maintaining the surface temperature of the copper alloy at 120 ° C. or lower in step S15, as described above, after sufficiently cooling in advance so that the surface temperature of the copper alloy becomes 20 ° C. or lower. It is not limited to the case of forging using
  • a temperature measurement mechanism such as a thermocouple is attached to the surface of the copper alloy being forged, and while constantly monitoring the measurement result of the temperature measurement mechanism, the temperature of the copper surface is controlled so that it will not always exceed 120 ° C. If the surface temperature exceeds 120 ° C., the operation may be interrupted, or the copper alloy may be water-cooled, air-cooled or allowed to cool.
  • FIG.5 (a) is a schematic diagram of the external appearance of the beryllium-copper forged bulk body which concerns on embodiment
  • FIG.5 (b) shows the applied pressure at the time of repeating pressurization under fixed amount of reduction.
  • FIG. 5C shows the change in the surface temperature immediately after repeated pressurization. The amount of one-time reduction during repeated pressurization was 18%, and the applied pressure was controlled so as not to exceed 1000 MPa ( ⁇ 1200 MPa).
  • the beryllium copper forged bulk body 1 obtained was not cracked or unevenly deformed in appearance.
  • 6 (a) to 6 (c) show the conventional method, that is, the overaging treatment (step S13 in FIG. 2) and the cooling treatment (steps S152, S154, S156) for the copper alloy after step S12.
  • the reduction amount was controlled to 33% (strain amount 0.40) so that the cumulative strain amount was in the range of 0.3 to 0.7.
  • the applied pressure is about 1300 MPa (> 1200 MPa)
  • the surface temperature immediately after repeated pressing reaches about 130 ° C. (> 130 ° C.). did.
  • FIGS. 7A to 7C are diagrams showing a method for measuring the hardness of the forged beryllium-copper bulk material according to the embodiment.
  • a cube-shaped beryllium copper forged bulk body 1 having a side of 100 mm is prepared, and the flat plate 2 is cut out so as to include the center portion and the surface portion (side end face) of the cube.
  • This test piece was obtained by a method according to JISZ2244 (Vickers hardness test-test method (corresponding international standard: ISO / DIS6507-1; 1995 Metallic-materials--Vickers-hardness-test--Part-1; Test-Method)).
  • FIG. 7 (b) shows the measurement results of the hardness of the copper alloy immediately after the forging process in step S15 in FIG. 2, and FIG. 7 (c) shows the beryllium copper as the final shape immediately after the aging process in step S16 in FIG. The measurement result of the hardness of a forged bulk body is shown.
  • FIG. 8 is a graph showing the measurement results of the hardness of a conventional forged beryllium copper bulk body not subjected to the processes of steps S13 and S15. As can be seen from FIG. 8, in the conventional forged beryllium copper bulk body, the hardness value greatly decreased from the side end face toward the center.
  • FIG. 9 shows an example of processing strain measurement results of a beryllium copper forged bulk body.
  • a flat plate 2a left side of the paper
  • a flat plate 2b right side of the paper
  • the warpage heights of the flat plates 2a and 2b are respectively compared.
  • the conventional flat plate 2a has warped of about 1 mm or more, the flat plate 2a according to the embodiment hardly warps.
  • FIG. 10 shows examples of fatigue life measurement results of the beryllium-copper forged bulk body 1 according to the embodiment and the conventional beryllium-copper forged bulk body.
  • the measurement was performed according to the JISZ2274 rotational bending fatigue test in a room temperature atmosphere using a No. 2-8 test piece.
  • Each plot shows a point at which fatigue fracture occurred.
  • the beryllium copper forged bulk body according to the embodiment it can be seen that the fatigue life is longer than that of the conventional bulk body.
  • FIG. 11 (a) and FIG. 11 (b) show an example of the ultrasonic deep damage test result of the forged beryllium copper bulk body according to the embodiment. 11 (a) and 11 (b), a forged beryllium copper forged bulk after processing after cutting the surface layer of a cubic beryllium copper forged bulk body with a side of 100 mm into a cube with a side of 70 mm. Ultrasound was sent to the body.
  • FIG. 11B when the forged beryllium-copper bulk material according to the embodiment is tested, a bottom echo peak with a thickness of 70 mm appears and double reflection also occurs in the vicinity of 140 mm. It can be seen that an echo peak appears. This indicates that the ultrasonic waves are not disturbed or attenuated by the internal structure of the beryllium copper forged bulk body. Compared to the case shown in FIG. 11 (a), since no noise appears in the entire waveform, it is presumed that the internal structure is more dense and uniform than the conventional forged beryllium copper bulk body. .
  • Table 1 and Table 2 show the difference in characteristics between the beryllium copper forged bulk body according to one embodiment of the present invention and the beryllium copper forged bulk body according to the comparative example (conventional example).
  • the material used in Table 1 is composed of Cu 100- (a + b) Be a Co b (0.4% ⁇ a ⁇ 2.0%, 0.15% ⁇ b ⁇ 2.8%, a + b ⁇ 3.5%).
  • a copper alloy was prepared. Each copper alloy was melted in a high frequency melting furnace to produce an ingot, and the obtained ingot was homogenized. The obtained ingot is processed by a forging process, and the oxide film formed on the surface is removed by cutting to form a cube shape having a side of 100 mm. Sample members A1 to A7, B1 to B7, A101 to A105, B101 to B105 and C101 to C103 were obtained.
  • Step S12 For the sample members A1 to A7, B1 to B7, A101 to A105, B101 to B105, and C101 to C103, the processing shown in steps S12 to S15 in FIG. Cold forging process).
  • “Discontinuous / continuous” in the column of “Overaging treatment” in Table 1 means that the solution treatment in Step S12 and the overaging treatment in Step S13 are as shown in FIGS. 3 (a) and 3 (b). Means the difference between the case of being carried out independently and discontinuously and the case of being carried out continuously.
  • the “maximum temperature before pressurization” in the “overaging treatment” column indicates the maximum value of the surface temperature of the copper alloy measured immediately before the cold forging process in step S15.
  • Maximum pressure in the column of “Pressurizing treatment” in Table 1 indicates the maximum pressure applied to the copper alloy by the forging device.
  • the “maximum temperature after pressurization” indicates the maximum value of the surface temperature of the copper alloy that gradually increases with repeated pressurization.
  • Hardness after aging in Table 1 shows the average value of the results of 25 points measured after returning to room temperature after aging treatment at 315 ° C. for 2 h.
  • Test strength in Table 2 is the result of a tensile test in the above-mentioned six directions performed according to JISZ2241, and the result of examining whether the average value and the six numerical values are within ⁇ 5%. is there.
  • a test piece used for the tensile test was obtained by cutting a flat plate including XY, YZ, and XZ planes from the center of the forged beryllium copper bulk body 1 of FIG. JISZ2241 (Metal Material Tensile Test Method) is machined so that the Y, Z axis direction, XY 45 °, YZ 45 °, XZ 45 °) coincides with the tensile axis. Measured according to
  • Shear band structure refers to a shear structure in which the phase of atoms (crystal grains) has shifted out of phase with a certain plane as a boundary. In particular, the phase shift in a strip shape in the direction of deformation as in this case. Refers to the organization where this occurs.
  • maintain substantially uniform hardness to the inside has been manufactured.
  • the aging end has a hardness of 393 to 405 and a center of 397 to 411, and the forged beryllium copper bulk body according to this embodiment It can be seen that the hardness is almost equal from the end to the inside, or the hardness between the center and inside changes within 10%.
  • the present invention is a machine structural component that requires durability and reliability, such as an aircraft bearing, a submarine cable repeater casing, a ship rotor shaft, an oilfield drilling collar, an injection mold, and a welding electrode holder. It is possible to use it.

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PCT/JP2009/053449 2008-03-28 2009-02-25 ベリリウム銅鍛造バルク体 WO2009119237A1 (ja)

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EP09725472.6A EP2264199B1 (en) 2008-03-28 2009-02-25 Forged beryllium-copper bulk material
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WO2013146309A1 (ja) 2012-03-27 2013-10-03 日本碍子株式会社 鍛造方法及び鍛造用金型
CN110291219A (zh) * 2016-12-15 2019-09-27 美题隆公司 具有均匀强度的经沉淀强化的金属合金制品
WO2019189613A1 (ja) 2018-03-28 2019-10-03 日本碍子株式会社 鍛造具
JP2021155837A (ja) * 2020-03-30 2021-10-07 日本碍子株式会社 ベリリウム銅合金リング及びその製造方法

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US20200362444A1 (en) * 2017-11-17 2020-11-19 Materion Corporation Metal rings formed from beryllium-copper alloys

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Publication number Priority date Publication date Assignee Title
WO2013146309A1 (ja) 2012-03-27 2013-10-03 日本碍子株式会社 鍛造方法及び鍛造用金型
KR20140129317A (ko) 2012-03-27 2014-11-06 엔지케이 인슐레이터 엘티디 단조 방법 및 단조용 금형
JPWO2013146309A1 (ja) * 2012-03-27 2015-12-10 日本碍子株式会社 鍛造方法及び鍛造用金型
US9586256B2 (en) 2012-03-27 2017-03-07 Ngk Insulators, Ltd. Forging method and forging die
CN110291219A (zh) * 2016-12-15 2019-09-27 美题隆公司 具有均匀强度的经沉淀强化的金属合金制品
WO2019189613A1 (ja) 2018-03-28 2019-10-03 日本碍子株式会社 鍛造具
KR20200120737A (ko) 2018-03-28 2020-10-21 엔지케이 인슐레이터 엘티디 단조 공구
US11529671B2 (en) 2018-03-28 2022-12-20 Ngk Insulators, Ltd. Forging tool
JP2021155837A (ja) * 2020-03-30 2021-10-07 日本碍子株式会社 ベリリウム銅合金リング及びその製造方法
US11746404B2 (en) 2020-03-30 2023-09-05 Ngk Insulators, Ltd. Beryllium copper alloy ring and method for producing same

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CN101981211A (zh) 2011-02-23
CN101981211B (zh) 2012-12-12
JP5416091B2 (ja) 2014-02-12
KR101467617B1 (ko) 2014-12-01
EP2264199A4 (en) 2015-07-08
EP2264199B1 (en) 2016-12-28
KR20100134619A (ko) 2010-12-23
US20100329923A1 (en) 2010-12-30
EP2264199A1 (en) 2010-12-22

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