WO2006082921A1 - LAITON α RENFORCE ET PROCEDE DE PRODUCTION DE CELUI-CI - Google Patents

LAITON α RENFORCE ET PROCEDE DE PRODUCTION DE CELUI-CI Download PDF

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Publication number
WO2006082921A1
WO2006082921A1 PCT/JP2006/301860 JP2006301860W WO2006082921A1 WO 2006082921 A1 WO2006082921 A1 WO 2006082921A1 JP 2006301860 W JP2006301860 W JP 2006301860W WO 2006082921 A1 WO2006082921 A1 WO 2006082921A1
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WIPO (PCT)
Prior art keywords
brass
annealing
mpa
reinforced
grain size
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PCT/JP2006/301860
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English (en)
Japanese (ja)
Inventor
Hiroshi Yamaguchi
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Mitsui Mining & Smelting Co., Ltd
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Application filed by Mitsui Mining & Smelting Co., Ltd filed Critical Mitsui Mining & Smelting Co., Ltd
Priority to US11/815,607 priority Critical patent/US20090120544A1/en
Priority to DE112006000331T priority patent/DE112006000331T5/de
Publication of WO2006082921A1 publication Critical patent/WO2006082921A1/fr

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Classifications

    • 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
    • C22C9/04—Alloys based on copper with zinc as the next major constituent
    • 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
    • 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
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B2001/221—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length by cold-rolling
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/005—Copper or its alloys
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B2003/008—Zinc or its alloys

Definitions

  • the present invention relates to a reinforced OC brass material that is excellent in strength and formability, has a balance between strength and formability, and maintains a certain level of stress relaxation characteristics, and a method for producing the same.
  • the conventional brass material has a drawback that if it is desired to obtain a material having higher strength by increasing the processing rate, the bending process becomes poor and the toughness is poor and the bending process becomes difficult. . In other words, when caulking to connectors, etc., it is often necessary to apply a strict bending force. ⁇ .) is 55
  • the processing method using oc brass as a strip is generally performed by semi-continuous forging, hot rolling and chamfering, followed by cold rolling and continuous rolling to a thickness that allows a continuous annealing process. It is cut into strips through the steps of annealing pickling, cold rolling, continuous annealing pickling and cold rolling. In this process, annealing and rolling may be repeated depending on the thickness, or annealing may be a batch method. There are various manufacturing processes, such as omitting the last rolling if dulling is desired, and during or after rolling and heat treatment, such as degreasing, pickling, straightening, cutting, plating, etc. Steps can be added. Such a conventional manufacturing process is hereinafter referred to as a “general manufacturing process” in the present application.
  • the annealing conditions of the above general manufacturing process are performed within a range of 480 ° C to 850 ° C as disclosed in Patent Document 1.
  • the grain size is generally set to ⁇ to 35 / ⁇ m.
  • the Vickers hardness (Hv) Will be 60-80.
  • the crystal grain size is generally 5 ⁇ to 60 / ⁇ ⁇ depending on the application, and the Vickers hardness ( ⁇ ) is 50 to 120.
  • general manufacturing process after the final annealing, the product is finished into a product strip by cutting after passing through the final cold rolling process. And in this application, what passed through this last cold rolling process is hereafter called "general material”.
  • Patent Document 2 As a method for increasing the strength of brass, a force generally known to use work hardening is disclosed in Patent Document 2, in which crystal grains are refined to increase the strength, and cold rolling is applied to this. A method of obtaining high strength by adding is disclosed.
  • Non-patent document 2 and non-patent document 3 disclose the method of crystal grain refinement.
  • Patent Document 2 discloses a method for producing brass having fine crystal grains.
  • it is necessary to repeatedly perform rolling at a large processing rate in multiple stages. Therefore, it is a technology that can be applied when trying to obtain a thin product.
  • it may be difficult to apply the rolling process under multiple conditions multiple times.
  • the contents disclosed in Patent Document 1 although there is a description of the final annealing, there is no disclosure even though the previous annealing conditions are important.
  • Non-Patent Document 4 reports the results of research on increasing the strength by refining crystal grains.
  • fine grains with a two-phase mixed structure force of a phase and ⁇ phase are obtained by strong processing and relatively low temperature annealing for a long time, and when this is further processed and annealed at low temperature, high strength is obtained.
  • a material with relatively good bending workability can be obtained.
  • the stress relaxation characteristics deteriorate as the crystal grains become finer, and that slight improvement is observed by low-temperature annealing.
  • Patent Document 1 JP-A-53-32819
  • Patent Document 2 Japanese Patent Application Laid-Open No. 2004-292875
  • Non-Patent Document 1 Published by Japan Copper and Brass Association Data book of copper products p. 19
  • Non-patent document 2 Copper and copper alloy 41, 1, 29
  • Non-patent document 3 Copper and copper alloy 43, 1, 21
  • Non-Patent Document 4 Journal of Copper Technology 39, 1, 128
  • Non-Patent Document 5 Japan Copper and Brass Association Data Book p. 226
  • Non-Patent Document 2 the case where annealing was performed at 230 ° CX for 17 hours, which showed the best resistance, was performed by cold working. From the heat-cured state to the state where it cannot be sufficiently softened by annealing, the annealing is stopped to improve bending workability and obtain a relatively high strength. The crystal structure obtained at this time has a 0.2% resistance to resistance ( ⁇ .) Of 534 MPa because a non-uniform recrystallization state is formed.
  • Patent Document 2 suggests a preferable example of a method for producing brass having an excellent balance between strength and bending workability.
  • the balance between concrete strength and bending workability can be considered, and in the evaluation of bending workability, the bending direction (Good Way) that is advantageous for obtaining good bending characteristics is adopted.
  • the inventors of the present invention have come up with a production condition for obtaining a fine crystal grain structure that is excellent in industrial productivity and can reduce variations in product quality. That is, the present invention satisfies the workability required for a general ⁇ -brass material, has a strength higher than that of a general material, and further, has a strength of a hard material of phosphor bronze, which is higher than that of a brass material, or higher than that of a hard material.
  • a method of manufacturing a reinforced O brass material that maintains a certain level of stress relaxation characteristics and a reinforced OC brass material obtained from this method. It is.
  • the present invention is a method for producing reinforced OC brass having a composition of copper 63 wt% to 75 wt%, the balance other than inevitable impurities being zinc.
  • a brass plate having a crystal grain size of 1 ⁇ -2 / ⁇ m was used as a starting plate material, which was cold rolled at a processing rate of 5% to 40% to form a cold rolled brass plate. It is characterized by low-temperature annealing of brass plate and adjusting 0.2% resistance ( ⁇ .: MPa) to 90% or more of the maximum value. O Provide a method for manufacturing brass.
  • the low temperature annealing is preferably performed at a temperature equal to or higher than the annealing temperature at which the 0.2% proof stress shows the maximum value in view of the dependency of the 0.2% proof stress on the annealing temperature.
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m as the starting plate material is a chamfered brass plate after hot rolling or a brass plate having a crystal grain size of 7 ⁇ to 200 / ⁇ m.
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m which is the starting plate material, is a hot-rolled chamfered brass plate or a brass plate having a crystal grain size of 7 m to 200 m as a raw material.
  • Vickers hardness (Hv) is adjusted to the range of 130-170 by recrystallization annealing after applying cold rolling at a processing rate of 80% -95% as a material, and 40% -95% It is also preferable to use the one in which the cold rolling process is carried out at the processing rate and the Vickers hardness (Hv) is adjusted in the range of 130 to 170 by recrystallization annealing.
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m which is the starting plate material, is made of a brass plate having a crystal grain size of 3 ⁇ m to 6 / zm as a raw material. It is also preferable to use a Vickers hardness (Hv) adjusted within the range of 130 to 170 by refining the cold rolling force at the processing rate and performing recrystallization annealing.
  • Hv Vickers hardness
  • the recrystallization annealing is preferably performed at 370 ° C to 650 ° C when continuous annealing is performed, and at 255 ° C to 290 ° C when batch annealing is performed.
  • the present invention is a reinforced OC brass having a composition of 63 wt% to 75 wt% copper obtained by the method for producing reinforced a brass, and the balance other than unavoidable impurities has a zinc strength, and has a tensile strength strength.
  • the reinforced brass has an Erichsen value (Er: mm) and 0.2% resistance ( ⁇ .: MPa).
  • X brass has the above-mentioned excellent physical properties stable and is also suitable for production on an industrial scale.
  • the manufacturing method of the reinforced ⁇ brass according to the present invention is a manufacturing method of reinforced OC brass having a composition in which the balance other than unavoidable impurities is zinc power with a copper particle of 1 wt.
  • a brass plate of ⁇ -2 / ⁇ m cold rolled at a processing rate of 5% to 40% to obtain a cold rolled brass plate, and this cold rolled brass plate is annealed at low temperature.
  • 2% resistance ⁇ .: MPa is adjusted to 90% or more of the maximum value.
  • the starting plate material can be made to have a more uniform grain size distribution after the subsequent cold rolling by making the grain size uniform to 1 m to 2 m by recrystallization treatment. The Then, cold rolling is added to the brass plate at a processing rate of 5% to 40% to obtain a cold rolled brass plate.
  • the processing rate in the cold rolling is less than 5%, the low temperature will be described later.
  • the yield strength is lowered even after annealing, the hardening of the mold progresses when the final cold rolling process rate exceeds 40% and the bending strength is MBRZt even though the yield strength is improved. It is difficult to obtain reinforced OC brass with a good mechanical property balance.
  • 0.2% strength resistance is used as an index of mechanical strength of reinforced ⁇ brass.
  • the mechanical strength of general materials is usually indicated by tensile strength and elongation.
  • the tensile strength is a value calculated from the maximum load force observed up to the break in the tensile test, and this maximum load value has already been subjected to tensile processing and is a factor that changes the cross-sectional shape and physical properties. Therefore, the present inventors thought that it was inappropriate to use tensile strength as an index of workability. Therefore, as an index that can be used to compare and evaluate the properties of the material itself before processing, it is mainly used as a design standard, and the 0.2% resistance ( ⁇ .: MPa) is adopted as an index of strength.
  • the low temperature annealing temperature when the low temperature annealing temperature is raised, the resistance increases with a loose peak, further decreases and then decreases rapidly. This is known as the low temperature annealing hardening phenomenon.
  • the reason why the 0.2% proof stress after low-temperature annealing is limited to a temperature that exceeds 90% of the maximum 0.2% proof stress obtained by the low-temperature annealing hardening phenomenon is to suppress the decrease in strength.
  • the force 0.2% proof stress is the temperature that shows the maximum value of 0.2% proof stress, but the peak width of the maximum 0.2% proof stress is narrow when viewed on the temperature axis or the time axis when the processing rate is low. When the processing rate is high, a broad and gentle peak can be obtained, so the condition for obtaining the maximum value is regarded as the heating condition for obtaining the maximum value over a range showing 99% or more of the maximum value. Is more practical.
  • the low-temperature annealing is preferably performed at a temperature equal to or higher than the annealing temperature at which the 0.2% proof stress shows the maximum value in view of the annealing temperature dependency of the 0.2% proof stress.
  • the low-temperature annealing performed refers to a process involving a so-called low-temperature annealing hardening phenomenon that does not simply refer to strain relief annealing performed at a low temperature.
  • the present inventor has found that the stress relaxation rate of around 55% of the work finish decreases from the annealing temperature that brings about the maximum value of 0.2% proof stress, decreases with increasing temperature, and settles to a certain level. Look at it! Therefore, as a condition for obtaining a stress relaxation rate threshold value of 52% or less, it is necessary to set the low-temperature annealing temperature to a temperature at which 0.2% resistance to the maximum value is higher or higher.
  • low temperature annealing is also a continuous method rather than a batch method
  • the furnace temperature is 250 ° C to 450 ° C
  • the plate passing time is 1 second to 10 seconds.
  • the advantage of continuous low-temperature annealing is that it is easy to reduce costs and ensure quality stability.
  • This low-temperature annealing is the final annealing, and is usually in the state of strips after the low-temperature annealing is completed.
  • batch-type annealing the strips are placed in a heating furnace in the form of a coil and are heated as they are. Therefore, the streaks are attached to the strips, and in the correction process before use as a product, it is necessary to correct up to the curl in addition to the distortion caused by rolling. However, effective correction becomes difficult.
  • the plate material is heated while traveling in the heating zone, and is wound into a coil after completion of the low-temperature annealing. Easy to obtain
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m which is the starting plate material, is made from a face-cut brass plate after hot rolling or a brass plate having a crystal grain size of 7 m to 200 m.
  • the large-diameter brass plate (annealed material) used as a raw material includes the case of hot rolled material.
  • the grain size of the crystal structure of the plate after hot rolling is 100 ⁇ m to 200 ⁇ m when a small test rolling mill is used.
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m which is the starting plate material, is a hot-rolled chamfered brass plate or a brass plate having a crystal grain size of 7 m to 200 m as a raw material.
  • Vickers hardness (Hv) is adjusted to the range of 130-170 by recrystallization annealing after applying cold rolling at a processing rate of 80% -95% as a material, and 40% -95% It is also preferable to use the one in which the cold rolling process is carried out at the processing rate and the Vickers hardness (Hv) is adjusted in the range of 130 to 170 by recrystallization annealing.
  • the brass plate having a crystal grain size of 1 ⁇ m to 2 ⁇ m as the starting plate material is made of a brass plate having a crystal grain size of 3 ⁇ m to 6 / zm as a raw material, and has a 70% to 95% It is also preferable to use a material whose Vickers hardness (Hv) is adjusted in the range of 130 to 170 by refining the cold rolling force with the processing rate and performing recrystallization annealing. If the crystal grain size before processing exceeds 6 m, even if cold rolling is applied at a processing rate of 70%, sufficient crystal grains cannot be refined and bending workability deteriorates.
  • Hv Vickers hardness
  • the average grain size is less than 3 m, it may be disadvantageous because the rolling pressure increases even if the subsequent processing rate is 70%. In addition, if the processing rate exceeds 95% and cold rolling is performed, cracks may occur at the ends during processing, which is not preferable.
  • the recrystallization annealing is preferably performed at 370 ° C to 650 ° C when continuous annealing is performed, and at 255 ° C to 290 ° C when batch annealing is performed.
  • the final recrystallization annealing is performed at a furnace temperature of 370 ° C. to 650 ° C. in continuous annealing.
  • the furnace temperature is less than 370 ° C, the feeding speed is Even if it is dropped and recrystallized, the moldability of the product obtained is deteriorated.
  • the recrystallization annealing time at this time is a force determined by the capacity of the furnace, the plate thickness, and the desired strength. In the case of normal industrial equipment, it is in the range of 2 to 120 seconds. If a practically appropriate time is to be determined, it is simply controlled by the hardness and determined so that the Vickers hardness (Hv) is 130 to 170, preferably 135 to 160.
  • the Vickers hardness (Hv) is less than 130, the recrystallized grain size is large, making it difficult to obtain the desired physical properties even if subsequent processing is performed. It becomes a structure with a higher remaining ratio of cold-worked structure than that of the structure, and strengthens it as a final product (the formability of X brass deteriorates).
  • An advantage of performing recrystallization annealing in a continuous manner is that it is easy to reduce costs and ensure quality stability.
  • the substantial temperature tends to be unevenly distributed due to the position in the furnace.
  • the value of [proof strength] Z [tensile strength] after final recrystallization annealing tends to be less than 80%, whereas the final recrystallization with the continuous heating method is used.
  • the value of [Yield Strength] Z [Tensile Strength] after crystal annealing becomes as high as 80% or more, and finer crystal grains can be obtained. Therefore, the continuous heating method has a better balance between the yield strength and forming processability of the reinforced OC brass obtained through the final cold rolling process and the low temperature annealing, which are the manufacturing methods according to the present invention, than the batch heating process. It becomes.
  • batch annealing is also applicable when the plate thickness is heavy or when a continuous annealing furnace is not provided. Industrially, it is usually held for about 30 minutes to 3 hours after the actual temperature of the coil reaches the set temperature. For this holding time, it is preferable to set the actual temperature to 255 ° C to 290 ° C. If the body temperature of the coil is less than 255 ° C, recrystallization to match the desired strength will result in irregular grain sizes (the horizontal axis is the logarithmic axis of the grain diameter). In the case of the particle size distribution chart, the distribution in which two or more peaks are observed), the bending kayakability is extremely deteriorated even by low-temperature annealing.
  • the present invention is a reinforced OC brass having a composition of 63 wt% to 75 wt% of copper obtained by the method for producing reinforced a brass, and the balance other than unavoidable impurities is a zinc force, and has a tensile strength strength. ⁇ 530MPa ⁇ 790MPa, 0. 2 0/0 ⁇ ( ⁇ .) mosquitoes S450MPa ⁇ 750MPa, 120. CX 10
  • a minimum bending radius (MBR: mm) without cracks is often used. Bending quesability is an important index in the process of forming the terminal.
  • the term “bending workability” is based on the premise that, in various bending tests, evaluation is performed by performing so-called Bad way bending in which the bending axis of right-angle bending is parallel to the rolling direction. Performing a bending test with the direction perpendicular to the rolling direction as the bending axis, so-called ⁇ Goood way '' bending, usually gives better results in comparison with Bad way bending in the case of brass. It was considered unsuitable for this. In this application, therefore, only Bad way bending is used as the evaluation method.
  • MBR Zt is a level that will become 1.0 or more 0.2% resistance ( ⁇ .) Exceeds 550MPa
  • the Japan Copper and Brass Association has established a test method (using a cantilever to measure the permanent deflection displacement due to bending).
  • a temperature of 120 ° C was selected as appropriate, and the treatment time was set to 100 hours because the difference could be evaluated with a force of 100 hours, which is 1000 hours in the test method.
  • the stress relaxation rate is examined, the data power of 40%, 40%, 36%, 40%, 48% to 52% It was found that it varies depending on the quality of additional U and the grain size.
  • the test piece is evaluated within 2 weeks after production in order to avoid the effects of changes over time. Therefore, the present inventor considers the fact that all of these are put into practical use and the fact that the customer dislikes the deterioration of the stress relaxation rate, and the stress relaxation rate required for the reinforced ⁇ brass according to the present invention.
  • the threshold was set at 52%.
  • the reinforced brass has an Erichsen value (Er: mm) and 0.2% resistance ( ⁇ .: MPa).
  • the minimum bending radius of right-angle bending becomes zero, and it cannot be used as an index of moldability to cover a wide range of strength.
  • the Eriksen value (Er: mm) is often used as an index of moldability! Therefore, in the present invention, the Eriksen value (Er: mm) is further used as an additional index. It was.
  • the inventor first collected 17 samples of 1Z2H, H, and EH materials of C2600 or C2680 shown in JIS standard, and 0.2% resistance ( ⁇ . MPa) and Erichsen value (Er: mm). And both
  • the Erichsen value is a numerical value obtained by the following Erichsen test (Erichsen Test), and is used as a standard for determining the deep drawability of a thin metal sheet.
  • Test equipment and test method standards JIS B 7777
  • the Erichsen value (Er: mm) of the reinforced a brass according to the present invention is 0.2% resistance ( ⁇ .
  • Equation 9 Force Satisfies Equation 9 over the entire range of 50MPa to 750MPa, and is at least 0.5mm or more when compared with the same general material that shows the same 0.2% resistance ( ⁇ .: MPa)
  • the bending strength of phosphor bronze can be expressed by the following equation (10).
  • the bending force resistance of phosphor bronze is less than 0.2% resistance ( ⁇ .) 590 MPa.
  • the force that MBRZt is 0.3 or less 0.2% resistance ( ⁇ .) MBRZt is 3 for 800MPa
  • the physical properties of the reinforced ⁇ brass according to the present invention are 0.2% strength ( ⁇ .) Force 50MPa to 750MP.
  • the reinforced ⁇ brass according to the present invention which satisfies Expression 11, takes into account that there is a certain variation in the quality of phosphor bronze, and 0.2% resistance ( ⁇ .: MPa) And bending Karoe
  • the average crystal grain size is generally 2 ⁇ m or less. This is a structure derived from the recrystallized structure, and has a recovery structure as described later.
  • the average crystal grain size is preferably 2 m or less.
  • the crystal structure of the reinforced ex brass according to the present invention described above is the structure of the recrystallized crystal grains using an optical microscope or a scanning electron microscope with a high magnification after electrolytic etching. It can be measured using a line segment method or a photographic comparison method.
  • the structural changes due to low-temperature annealing can be remarkably distinguished when observed using SEM-EBSP.
  • image processing is performed in which the image quality value is less than a certain value (distortion cancellation is less than a certain value)
  • the recovered grains can be recognized as bright grains, and the outline gradually becomes more progressive as recovery progresses.
  • With smooth power the recrystallized grains can be recognized as bright grains with annealing twins. And the bending workability is good!
  • the structure of reinforced ex brass is a microstructure in which grains released from strain (recovered grains or recrystallized grains) and grains not released by low temperature annealing are mixed. Is similar to a fine two-phase mixed structure, which is considered to promote inhomogeneous sliding and improve bending workability.
  • the improvement in stress relaxation characteristics due to low-temperature annealing corresponds to an increase in the area ratio of recovered or recrystallized grains, which ensures favorable stress relaxation characteristics with changes in the texture. That means it is essential.
  • the enhancement ⁇ according to the present invention ⁇ Brass has a fine grain size of 1 ⁇ m to 2 m, so it has high fatigue strength and stress corrosion cracking resistance, and has a small bending deflection coefficient!
  • Table 1 shows the chemical composition of brass ingots used for production and evaluation in the following examples and comparative examples.
  • ingot 1 to ingot 6 are samples obtained by a semi-continuous forging method at a manufacturing site forging factory.
  • Ingot 7, ingot 8, and ingot 9 were obtained by melting in a laboratory melting furnace and forging to 30 mm x 100 mm x 200 mm with a mold.
  • the ingots 1 to 9 are made of 65.2 wt% to 74.2 wt% of copper, and satisfy the conditions of the present invention if they are composed of the balance zinc and inevitable impurities. Furthermore, in the following examples, any of the ingots shown in Table 1 above was used, and the manufacturing conditions consisting of the following steps (a) to (e) shown in Table 2 were applied to form a brass strip. ! / (a) Raw material preparation
  • the ingot 1 obtained above was hot-rolled and then chamfered, cold-rolled and annealed to obtain a raw material with a thickness of 1.8 mm.
  • the raw materials and starting plate 1 were all manufactured on the production line at the site until annealing (c) before the final cold rolling process. Thereafter, the processing conditions applied to Example 1 and Example 2 are shown together with Example 3 in Table 2 in comparison with Comparative Example 1 and Comparative Example 2.
  • Table 2 the previous annealing (a: annealing before recrystallization annealing before final cold rolling) and annealing before final processing (c: recrystallization annealing before final cold rolling) are on-site as described above. It is continuous annealing in the production line.
  • the temperature described here is the set temperature of the furnace.
  • the common starting plate 1 can be used up to the recrystallization annealing before the final cold rolling.
  • the starting plate 1 that also obtained the above-mentioned force was subjected to cold rolling (d) at a processing rate of 10% using an experimental cold rolling mill to form a cold rolled brass plate, and further cooled in a salt bath at a low temperature.
  • Annealing (e) It was.
  • the annealing time in the salt bath is set to a short time of 2 seconds to resemble continuous annealing, and the temperature of the salt bath is set to Example 1–1, 1–2, 1–3 at 280 ° C and 340 ° C, respectively. 420 ° C.
  • the tensile strength is 532 MPa to 556 MPa
  • the resistance is 458 MPa to 504 MPa
  • the Erichsen value ( ⁇ . Force is also calculated) is 8.6 mm (8.3 mm) to 8. 8m
  • Example 2 the same starting plate material 1 as in Example 1 was subjected to cold rolling (d) at a processing rate of 24% using a laboratory cold rolling mill to form a cold rolled brass plate, and further cooled in a salt bath.
  • Annealed (e) The annealing time in the salt bath was set to a short time of 2 seconds to resemble continuous annealing, and the salt bath temperature was set to 260 for each of Examples 2-1, 2- 2, 2-3, and 2-4. C, 280 ° C, 300. C, 340. C.
  • the tensile strength was 667 MPa to 680 MPa
  • the meta force was 622 MPa to 638 MPa
  • the Erichsen value was 6.8 mm
  • the crystal grain size after the final pre-annealing (b) obtained in these examples and comparative examples was about 2 ⁇ m, and the crystal grain size after the final cold rolling cage (d) was 1 ⁇ m. .
  • ingot 2 was used, and after hot rolling, it was chamfered (a) to obtain a raw material having a thickness of 11.5 mm. Then, a preliminary test was performed by changing the processing rate and the annealing temperature to obtain an annealing softening curve.
  • the annealing time in the salt bath used is 10 seconds.
  • Figure 2 shows the annealing softening curve obtained here. According to Fig. 2, the Vickers hardness (Hv) of the recrystallized annealed material is stable at about 150 except for those with a processing rate of 70%.
  • the cache structure remains up to 430 ° C, and at 450 ° C, the maximum grain size is 10 ⁇ m and the grain size is less than 3 / zm. Has a mixed crystal structure.
  • the crystal grain size was approximately 2 ⁇ m.
  • the plate material that had been cold-rolled (b) at a processing rate of 95% was recrystallized in a salt bath at 430 ° C for 10 seconds using a cold rolling mill for experiments.
  • the starting plate was obtained by annealing (c).
  • a cold rolled casing (d) was added to a thickness of 0.52 mm at a rate of 10% to obtain a cold rolled brass sheet, which was annealed at a low temperature for 2 seconds in a 320 ° C salt bath.
  • the strength of the ⁇ brass material is 557 MPa, 0.2% resistance ( ⁇ .) Is 499 MPa, Erichsen
  • Example 4 to Example 8> In these examples, as shown in Table 4, ingot 2 to ingot 6 were used corresponding to each example, and everything from forging to final low-temperature annealing was performed using an on-site production line. First, a plate material that was 11.5 mm thick after face milling after hot rolling was subjected to cold rolling at a processing rate of 84% to 1.8 mm, and the previous annealing shown in Table 4 (a: annealing of the strip) ) To obtain a raw material, cold rolling (b) was added again, and final recrystallization annealing (c) was performed to obtain a sheet material.
  • Example 8 is further subjected to cold rolling and recrystallization annealing before the final recrystallization annealing (described in the upper part of Table 4). Then, a final cold rolling process (d) was added to these to form a cold rolled brass sheet, and then a low temperature annealing (e) was performed to obtain a product.
  • the low-temperature annealing conditions were as follows. In Example 4, continuous annealing was performed with the furnace temperature set at 420 ° C. This continuous annealing condition is set to 0.2%
  • the value is set to 0.3.
  • Example 5 the specimen at the stage after the previous annealing (a: strip annealing) in Example 5 was used as a raw material, and cold rolling (b) ) This strip is subjected to final recrystallization annealing (c) for 10 seconds in a salt bath at 420 ° C to obtain a starting plate, and then cold rolling (d) is added at a processing rate of 30% to cold rolled brass.
  • the plate was subjected to low temperature annealing (e) at 280 ° C for 10 seconds.
  • the tensile strength of the obtained reinforced ⁇ brass material is 651 MPa, 0.2% resistance ( ⁇ .) Is 601 MPa, elongation is 6.9%, Erichsen value (calculated from ⁇ .) Is 7.
  • ingot 7 to ingot 9 are used in correspondence with each example, and after hot rolling in a laboratory to obtain a crystal grain size of 0.15 mm, a processing rate of 86% Then, cold rolling (b) was performed at a processing rate of 78% using a raw material that had been subjected to cold rolling and then recrystallized annealing (a) under the condition that the crystal grain size was 5 m. added.
  • the plate material thus obtained was subjected to recrystallization annealing (c) for 2 hours at an actual temperature of 270 ° C to obtain a starting plate material, and a final cold rolling process (d) with a processing rate of 25% was added to perform cold A rolled brass plate was subjected to final recrystallization annealing (e) at an actual temperature of 205 ° C. All the low-temperature annealing at this time is carried out using a full furnace while measuring the actual temperature.
  • the tensile strength was 671 MPa to 681 MPa
  • the galvanic resistance was 629 MPa to 640 MPa
  • the Erichsen value (value calculated for ⁇ . Force) was 6. 7mm (6.7 mm) to 7
  • Example 1 the first low temperature annealing condition was changed with respect to Example 1 and Example 2, and the same was performed.
  • Table 2 shows the conditions.
  • Comparative Example 1 The same starting plate material 1 used in the examples was subjected to cold rolling at a processing rate of 10% using an experimental cold rolling mill, and further annealed at a low temperature in a salt bath. In Comparative Example 14 the low-temperature annealing was not performed. In Comparative Examples 15 and 16, the annealing time in the salt bath was set to 2 seconds as in the example, and the salt bath temperature was 240 ° C. 260 ° C. As a result of evaluating the physical properties of the obtained samples, the tensile strength was 547 MPa to 559 MPa, the resistance to 495 MPa to 499 MPa, the Erichsen value (calculated from ⁇ . Force) was 8.5 mm (8.2 mm) to 9. lmm (8.3 m
  • Comparative Example 2 The same starting plate material 1 used in Example 1 and Example 2 was subjected to cold rolling at a processing rate of 24% using a laboratory cold rolling mill, and further annealed at low temperature in a salt bath. did. In Comparative Example 25, low-temperature annealing was not performed. In Comparative Examples 2-6 and 2-7, the annealing time in the salt bath was set to 2 seconds, which was the same as in the example, and the temperature of the salt bath was set to 240 ° C and 420 ° C.
  • the tensile strength is 613 MPa to 670 MPa
  • the Erichsen value (value calculated from ⁇ . Force) is 7.3 mm (7. Omm) to
  • Comparative Example 3 Here, an ingot 7 was used, and a sample having the same resistance to that of Example 11 was prepared in a laboratory, which was similar to the conventional process. That is, this sample is hot rolled, cold After annealing to obtain a crystal grain size of 35 m after rolling the roll, cold rolling was applied at a processing rate of 53%. The subsequent recrystallization annealing was performed for 20 seconds using a 650 ° C salt bath to resemble the continuous annealing in the conventional process. As a result, the crystal grain size after final recrystallization annealing was 15 m. The final cold rolling force was added at a processing rate of 65%.
  • MBRZt (a. The value that calculated the force) that is an index of bending caloe is 2.4 (0. 9), which is bad.
  • C2680 Cu / Zn: 65% / 35%) and C2600 (Cu / Zn: 70% / 30%) H and C2680 (CuZZn: 65% Z35%) EH Evaluated as an example.
  • the brass materials of these reference examples were subjected to final cold rolling at a processing rate of 25% 17% 35% after recrystallization annealing, and were not subjected to low temperature annealing.
  • the evaluation results are tensile strength force ⁇ 486MPa 567MPa 0. 2 0/0 ⁇ ( ⁇ .) Force 437MPa 524MPa, stress Yuru ⁇ Roritsu
  • the force was 36% 52%, and the Eriksen value (Er) was 6.9 mm 8.3 mm. Details are shown in Table 7.
  • the mechanical strength and the stress relaxation value are satisfied, but the following Equation 17 regarding M BRZt and the following Equation 18 regarding the Eriksen value (Er) are not satisfied.
  • the reinforced ex brass according to the present invention has a general ex brass composition in terms of composition.
  • an appropriate rolling process and heat treatment which is the manufacturing method according to the present invention, the strength and molding strength of phosphor bronze, which is equivalent to or superior to phosphor bronze, is ineffective in conventional brass. It shows the balance.
  • Such reinforced ⁇ brass is suitable for electronic parts such as connectors and mechanical parts, and can be supplied as an inexpensive material.
  • the method for producing reinforced ⁇ brass according to the present invention can be used as it is without any improvement in the conventional rolling production line, and does not require any special equipment investment. Therefore, efficient production of high-quality reinforced alpha brass on an industrial production scale is possible.
  • FIG. 1 shows the relationship between the low-temperature annealing temperature obtained from Example 1, Example 2, Comparative Example 1 and Comparative Example 2, 0.2% resistance ( ⁇ .), And stress relaxation rate. It is a figure.

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Abstract

L’invention concerne un laiton α renforcé qui, par rapport à un laiton conventionnel, présente un excellent équilibre en termes de limite d’élasticité élevée et d'aptitude au moulage sans détérioration des caractéristiques de relaxation en contrainte ; un procédé de production de celui-ci. Par conséquent, on utilise un laiton α renforcé produit en fournissant une plaque de départ obtenue en effectuant un recuit par recristallisation d’un laiton α renforcé constitué de 63 à 75 % en poids de cuivre, le reste étant du zinc et des impuretés inévitables, de façon à avoir un diamètre des particules de cristal de 1 à 2 µm, en effectuant un laminage à froid de la plaque de départ à un rapport de réduction de 5 à 40 %, et en effectuant un recuit à basse température en amenant la valeur maximale de 0,2 % de limite d’élasticité (σ0,2: MPa) de façon à ce que la limite d’élasticité de 0,2 % (σ0,2 MPa) soit ajustée à 90 % de la valeur maximale et soit comprise entre 450 et 750 MPa et de façon à ce que le rayon de pliage minimum (MBR)/épaisseur de plaque (t) et la limite d’élasticité de 0,2 % (σ0.2: MPa) répondent à la relation : MBR/t ≤ 0,0125´σ0,2 - 6,7, et de préférence de façon à ce que la valeur Erichsen (Er : mm) et la limite d’élasticité de 0,2 % (σ0,2: MPa) répondent à la relation : Er ³ -0,011´σ0,2 + 13,7.
PCT/JP2006/301860 2005-02-04 2006-02-03 LAITON α RENFORCE ET PROCEDE DE PRODUCTION DE CELUI-CI WO2006082921A1 (fr)

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US11/815,607 US20090120544A1 (en) 2005-02-04 2006-02-03 Strengthened Alpha Brass and Method for Manufacturing the Same
DE112006000331T DE112006000331T5 (de) 2005-02-04 2006-02-03 Verfestigtes α-Messing und Verfahren zu dessen Herstellung

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EP2592163B1 (fr) * 2010-07-05 2017-09-13 YKK Corporation Produit d'alliage cuivre-zinc et procédé de fabrication d'un produit d'alliage cuivre-zinc
JP5889698B2 (ja) * 2012-03-30 2016-03-22 株式会社神戸製鋼所 耐応力緩和特性に優れるＣｕ−Ｚｎ合金板及びその製造方法
CN104593706B (zh) * 2013-10-31 2017-01-18 宁波金田铜业(集团)股份有限公司 黄铜线材的冷连轧方法

Citations (2)

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Publication number Priority date Publication date Assignee Title
JPS5447823A (en) * 1977-09-17 1979-04-14 Diehl Brass material and method of making same
JP2004292875A (ja) * 2003-03-26 2004-10-21 Sumitomo Kinzoku Kozan Shindo Kk 結晶粒を微細化した７０／３０黄銅とその製造方法

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JPH11189856A (ja) * 1997-10-24 1999-07-13 Toto Ltd 黄銅材、黄銅管材及びそれらの製造方法
US20050039827A1 (en) * 2003-08-20 2005-02-24 Yoshinori Yamagishi Copper alloy having excellent corrosion cracking resistance and dezincing resistance, and method for producing same

Patent Citations (2)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS5447823A (en) * 1977-09-17 1979-04-14 Diehl Brass material and method of making same
JP2004292875A (ja) * 2003-03-26 2004-10-21 Sumitomo Kinzoku Kozan Shindo Kk 結晶粒を微細化した７０／３０黄銅とその製造方法

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