CN115821106B - Copper-zirconium alloy plate strip and preparation method thereof - Google Patents
Copper-zirconium alloy plate strip and preparation method thereof Download PDFInfo
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- 229910001093 Zr alloy Inorganic materials 0.000 title claims abstract description 42
- XTYUEDCPRIMJNG-UHFFFAOYSA-N copper zirconium Chemical compound [Cu].[Zr] XTYUEDCPRIMJNG-UHFFFAOYSA-N 0.000 title claims abstract description 42
- 238000002360 preparation method Methods 0.000 title description 8
- 238000005096 rolling process Methods 0.000 claims abstract description 54
- 239000002245 particle Substances 0.000 claims abstract description 14
- 238000000034 method Methods 0.000 claims abstract description 12
- 229910052760 oxygen Inorganic materials 0.000 claims abstract description 5
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 230000032683 aging Effects 0.000 claims description 54
- 238000010438 heat treatment Methods 0.000 claims description 47
- 238000005098 hot rolling Methods 0.000 claims description 19
- 239000010949 copper Substances 0.000 claims description 18
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims description 15
- 229910052802 copper Inorganic materials 0.000 claims description 15
- 229910001369 Brass Inorganic materials 0.000 claims description 9
- 239000010951 brass Substances 0.000 claims description 9
- 238000005266 casting Methods 0.000 claims description 7
- 238000004519 manufacturing process Methods 0.000 claims 3
- 239000000463 material Substances 0.000 abstract description 6
- 239000000956 alloy Substances 0.000 description 37
- 229910045601 alloy Inorganic materials 0.000 description 36
- 230000000052 comparative effect Effects 0.000 description 25
- 239000013078 crystal Substances 0.000 description 11
- 239000011159 matrix material Substances 0.000 description 10
- 238000004321 preservation Methods 0.000 description 9
- 230000000694 effects Effects 0.000 description 7
- 238000005482 strain hardening Methods 0.000 description 7
- 229910000881 Cu alloy Inorganic materials 0.000 description 6
- 239000000047 product Substances 0.000 description 5
- 238000001556 precipitation Methods 0.000 description 4
- 238000003723 Smelting Methods 0.000 description 3
- 230000002411 adverse Effects 0.000 description 3
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- 230000007547 defect Effects 0.000 description 3
- 229910052751 metal Inorganic materials 0.000 description 3
- 239000002184 metal Substances 0.000 description 3
- 230000006911 nucleation Effects 0.000 description 3
- 238000005728 strengthening Methods 0.000 description 3
- 230000035882 stress Effects 0.000 description 3
- 238000009864 tensile test Methods 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 238000001514 detection method Methods 0.000 description 2
- 230000018109 developmental process Effects 0.000 description 2
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- 238000003801 milling Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000004458 analytical method Methods 0.000 description 1
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- 238000001887 electron backscatter diffraction Methods 0.000 description 1
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Abstract
The copper-zirconium alloy plate strip disclosed by the invention comprises the following components in percentage by mass: 0.05 to 0.5 weight percent of O: less than or equal to 10ppm, and the balance of Cu and unavoidable impurities; the number of the precipitated phase particles containing O is expressed as A, and A is less than or equal to 5/mu m on the section of the plate strip perpendicular to the rolling direction 2 . According to the invention, by adjusting the addition amount of Zr and the content of O element, the number of O-containing precipitated phase particles on the section of the strip material perpendicular to the rolling direction is controlled, so that the strength and cold processing performance of the strip material can be improved while the good conductivity and excellent high temperature resistance of the strip material are ensured. The tensile strength of the plate strip is above 350MPa, the conductivity is above 85% IACS, and the softening temperature is more than or equal to 500 ℃; elongation in width direction delta w Elongation delta from length direction l Satisfy delta w /δ l And the temperature is more than or equal to 0.6, the cold processing performance is good, and cracks are not easy to generate in the cold processing process.
Description
Technical Field
The invention belongs to the technical field of copper alloy, and particularly relates to a copper-zirconium alloy plate strip and a preparation method thereof.
Background
The copper-based alloy has better physical and chemical properties such as electric conductivity, heat conductivity and corrosion resistance, is widely applied in the fields of electronics and the like, and particularly relates to multiple purposes of electronic parts such as connectors, lead terminals, switches and the like. Along with the development of scientific technology, electronic and electric elements are gradually miniaturized and light, the current density flowing in the use process of the elements is higher and higher, and meanwhile, the elements are required to have longer service life under high-temperature working conditions along with heating, so that quite high requirements are put on the conductivity and high-temperature resistance of the materials.
The copper-zirconium alloy has good high-temperature resistance as a high-conductivity copper alloy, but is difficult to maintain good strength and cold workability on the premise of ensuring the above properties, because: on the one hand, for copper alloys, the conductivity and strength are mutually exclusive, for example, copper-zirconium alloys are precipitation-strengthened alloys, which form finely dispersed intermetallic particles in the copper matrix during the preparation process, thereby improving the mechanical properties of the alloy and at the same time causing a reduction in the conductivity; on the other hand, uneven strain may cause local stress concentration during formation of the compound due to the difference in melting points of the constituent elements, and defects and cracks may occur during the subsequent cold working.
At present, development of a high-conductivity heat-resistant copper alloy material is urgently needed, good strength and cold processing performance are required, and the material can meet the increasing performance requirements of electronic and electric elements, and is not easy to crack in the cold processing process. In view of the object, the invention provides a copper-zirconium alloy plate strip and a preparation method thereof.
Disclosure of Invention
The first technical problem to be solved by the invention is to provide a copper-zirconium alloy plate strip which has excellent high temperature resistance and good electric conductivity, strength and cold workability.
The invention solves the first technical problem by adopting the technical scheme that: a copper-zirconium alloy plate strip comprises the following components in percentage by massr:0.05 to 0.5 weight percent of O: less than or equal to 10ppm, and the balance of Cu and unavoidable impurities; the number of the precipitated phase particles containing O is expressed as A, and A is less than or equal to 5/mu m on the section of the copper-zirconium alloy plate strip perpendicular to the rolling direction 2 。
Zr is taken as a main alloy element, dissolved into a copper matrix through solution treatment to form supersaturated solid solution, and then the solid solution is decomposed into a dispersed precipitated phase in the heat treatment process. The proper amount of Zr element can greatly reduce the grain boundary energy and generate solute drag and second phase pinning grain boundary, thereby improving heat resistance and strength; and the solubility of Zr in the Cu matrix is very low, the influence of the low-solubility alloy element Zr on the overall conductivity of the alloy is very limited, and the good conductivity of the alloy can be ensured. If the Zr content is too high, the size of the precipitated phase is increased and enrichment is generated, so that the conductivity of the alloy is rapidly reduced, and the cold workability of the alloy is deteriorated; if the Zr content is too low, the effect of precipitation strengthening cannot be obtained. Therefore, the Zr content in the copper-zirconium alloy plate strip is controlled within the range of 0.05wt% to 0.5 wt%.
The O element in the alloy exceeds a certain content to produce adverse effect, and the high copper alloy has larger tendency of inhalation phenomenon in the smelting process, so that the oxygen content of the alloy melt exceeds the standard, on one hand, the excessive burning loss of the alloy element can be aggravated, and on the other hand, defects such as inclusion and the like can be generated, and the subsequent processing is influenced. In addition, if the O content is too high, the mechanical properties of the alloy are adversely affected, so that the O content of the copper-zirconium alloy plate strip of the present invention can be strictly controlled to 10ppm or less by means of vacuum casting, a high-purity covering agent, a deoxidizer, or the like.
The copper-zirconium alloy plate strip introduces dispersed precipitated phase particles and precipitation and dispersion strengthening effects brought by the dispersed precipitated phase particles through alloy elements, and can improve the strength and cold processing performance of the plate strip while influencing the conductivity and high temperature resistance of the alloy as low as possible. Zr element in the alloy can form precipitated phases with uneven morphology and size after aging heat treatment, and the precipitated phases are distributed in the crystal and the crystal boundary of the matrix. Wherein the size of the precipitates distributed in the crystal is relatively fine and uniformEven, most of them are round or needle-like structures; the size of the precipitates distributed at the grain boundaries is large, and with a certain degree of O element enrichment, many triangular grain boundaries are formed at the grain boundary connection, and excessive triangular grain boundaries tend to undergo severe cracking during thermal deformation, causing deterioration of cold workability, so that the number of O-containing precipitated phase particles should be controlled as small as possible. The invention controls the number A of the O-containing precipitated phase particles on the section of the copper-zirconium alloy plate strip vertical to the rolling direction to be less than or equal to 5/mu m 2 The precipitated phase enriched in the grain boundary is reduced, and the whole precipitated phase is more uniformly dispersed in the crystal. When the A value is at a lower level, the tendency of the alloy to undergo uneven strain and localized stress concentration is reduced, whereas when the A value is too high, the alloy may be subjected to cold working to cause significant defects or even cracking.
Preferably, the average grain size in the microstructure of the copper-zirconium alloy sheet strip is 50 μm or less. The copper-zirconium alloy plate strip has a high-degree fine-grain microstructure, grains do not grow up completely, good strength can be obtained on the premise of not reducing toughness, and the comprehensive mechanical properties of the alloy can be effectively improved by matching with the dispersed precipitated phases.
Preferably, the area ratio S of the Gaussian texture in the microstructure of the copper-zirconium alloy plate strip g Area ratio S of brass texture b And the area ratio S of the copper texture c Meets the requirement of 0.5 to less than or equal to S g +S b )/S c Less than or equal to 1.5. When the area ratio of the copper-type texture with relatively low plasticity is too high, and the area ratio of the gaussian texture and the brass texture with good plasticity is too low, the tendency of uneven strain of the alloy is increased, the anisotropy of elongation is large in cold working, and fracture is seriously possibly caused; conversely, when the area ratio of the copper-type texture is too low and the area ratio of the gaussian texture and the brass texture is too high, the plasticity of the alloy is improved, but the strength and the conductivity are deteriorated. The area ratio of the Gaussian texture, the brass texture and the copper texture in the microstructure of the copper-zirconium alloy plate strip is controlled, so that the alloy plate strip can obtain good strength and excellent high temperature resistanceThe degree of uneven strain is reduced and the stress concentration is relieved, thereby ensuring good cold workability. Therefore, the area ratio S of the Gaussian texture in the microstructure of the copper-zirconium alloy plate strip is required to be controlled g Area ratio S of brass texture b And the area ratio S of the copper texture c Meets the requirement of 0.5 to less than or equal to S g +S b )/S c ≤1.5。
Preferably, the copper-zirconium alloy plate strip further comprises 0.01 to 1.0 weight percent of X in total, wherein X is at least one selected from Mg, cr, mn, si, ni, fe, B, P, RE.
The X element can play a role in strengthening to a certain extent, and can play a role of a deoxidizer in the casting process or serve as a nucleation center to improve the nucleation rate of the alloy, so that the purposes of purifying the melt and refining grains are achieved. The reduced oxygen content of the alloy melt reduces the tendency of oxide inclusions to occur; the fine-grain cast ingot provides good initial conditions for processing the plate and strip finished product, and is beneficial to improving the mechanical property and cold processing property of the copper-zirconium alloy plate and strip. When the content of the optional element X is less than 0.01 weight percent, the effects of purifying the melt and refining grains are not obvious; when the content is more than 1.0wt%, the conductivity of the alloy is greatly adversely affected by the excessive X element, so that the content of the X element is controlled to be 0.01wt% to 1.0wt%.
The tensile strength of the copper-zirconium alloy plate strip is above 350MPa, the conductivity is above 85% IACS, and the softening temperature is more than or equal to 500 ℃; the elongation percentage of the copper-zirconium alloy plate strip in the width direction is delta w Elongation in the longitudinal direction was δ l Both satisfy delta w /δ l ≥0.6。
The second technical problem to be solved by the invention is to provide a preparation method of a copper-zirconium alloy plate strip.
The invention solves the second technical problem by adopting the technical proposal that: the preparation method of the copper-zirconium alloy plate strip comprises the following process flows: casting, hot rolling, rough rolling, primary aging heat treatment, intermediate rolling, secondary aging heat treatment and finish rolling; the temperature of the primary aging heat treatment is 440-600 ℃, and the temperature of the secondary aging heat treatment is 300-440 ℃.
The temperature of the primary aging heat treatment is controlled to be 440-600 ℃, and the temperature of the secondary aging heat treatment is controlled to be 300-440 ℃. The primary aging heat treatment adopts a higher temperature of 440-600 ℃, the supersaturation degree of solute atoms of the alloy in the early aging stage is larger, a large number of dislocation and deformation zones form a highly uniform nucleation area in a matrix, the solute atoms are gradually gathered in a crystal boundary and a crystal interior by driving force caused by deformation to generate a precipitated phase, the higher primary aging heat treatment temperature provides enough internal energy, so that the precipitated phase is diffused at a higher speed on the premise that crystal grains are not obviously coarsened, the precipitation amount is increased, the distribution is more uniform, and meanwhile, the tendency of the precipitated phase in the form of coarse O-containing precipitated phase is lower, and the pinning effect on dislocation is more obvious. The secondary aging heat treatment is further reduced in temperature compared with the primary aging heat treatment, and the secondary aging heat treatment after the middle rolling can eliminate the influence of work hardening to a certain extent, so that the accumulated energy of severe plastic deformation can be released, and meanwhile, the precipitated phase can be fully precipitated and dispersed in the alloy matrix, and the size is more uniform and finer, so that the alloy strength and plasticity are improved on the premise of keeping higher conductivity.
Preferably, the total heat preservation time of the primary aging heat treatment and the secondary aging heat treatment is not less than 10 hours. In order to enable solute atoms in the alloy matrix to be separated out more thoroughly, enough heat preservation time is required to be given to ensure that the solute atoms are diffused effectively, so that the electric conductivity and cold processing performance of the copper-zirconium alloy plate and strip finished product are prevented from being deteriorated.
Preferably, the initial temperature of the hot rolling is 880 to 1000 ℃, and the total working rate of the hot rolling is 90% or more. The initial temperature of hot rolling is controlled between 880 ℃ and 1000 ℃ to ensure that alloy elements are fully dissolved into a copper matrix and grains do not grow. When the initial temperature of hot rolling is lower than 880 ℃, the fluidity of the metal melt is poor, the solute diffusion is insufficient, the deformation resistance is increased in the hot rolling process, and the cracking is easy to cause; when the initial temperature of hot rolling is higher than 1000 ℃, oxidation or excessive burning of the alloy element is caused, resulting in serious influence on the quality of the hot rolled stock. The total processing rate of the hot rolling is controlled to be more than 90 percent so as to further prepare for forming precipitated phases in the subsequent plate and strip finished products and reduce the enrichment tendency of coarse precipitated phases at the grain boundary. And meanwhile, enough distortion energy is provided to promote the transformation of copper type texture in the hot rolled blank so as to control the texture proportion in the finished product to meet the requirements.
Because rough rolling is arranged between hot rolling and primary ageing heat treatment, the method plays a role in providing driving force for the subsequent ageing heat treatment besides primarily adjusting the size of the plate strip. With the increase of the cold deformation degree of rough rolling, crystal grains are broken, the size is gradually reduced, dislocation in the crystal grains is continuously accumulated, the driving force of aging precipitation of the alloy is improved from inside, and the generation of precipitated phases is effectively promoted. After the primary aging heat treatment, the precipitated phase is gradually generated in the aging heat treatment process, the further cold deformation increases the resistance of dislocation movement, and the work hardening phenomenon occurs, so that the mechanical properties of the alloy are further enhanced. If the total working ratio of rough rolling is lower than the sum of the total working ratio of intermediate rolling and the total working ratio of finish rolling, the sufficient driving force cannot be provided for aging heat treatment, so that insufficient diffusion of precipitated phases occurs, local enrichment occurs, the cold working performance of the plate strip is reduced, meanwhile, the work hardening effect of the plate strip is overlarge, the electron scattering effect is aggravated, and the electric conductivity of the final plate strip product is sharply reduced. Therefore, preferably, the total reduction ratio of the rough rolling is not less than the sum of the total reduction ratio of the intermediate rolling and the total reduction ratio of the finish rolling.
Compared with the prior art, the invention has the following advantages: the invention controls the number A of precipitated phase particles containing O to be less than or equal to 5/mu m on the section of the copper-zirconium alloy plate strip vertical to the rolling direction by adjusting the addition amount of Zr and the content of O element 2 The copper-zirconium alloy plate strip has good conductivity and excellent high temperature resistance, and meanwhile, the strength and cold processing performance of the copper-zirconium alloy plate strip can be improved. The tensile strength of the copper-zirconium alloy plate strip is above 350MPa, the conductivity is above 85% IACS, and the softening temperature is more than or equal to 500 ℃; the copper-zirconium alloy plate stripThe elongation in the width direction of the material was delta w Elongation in the longitudinal direction was δ l Both satisfy delta w /δ l And the temperature is more than or equal to 0.6, the cold processing performance is good, and cracks are not easy to generate in the cold processing process.
Detailed Description
The present invention is described in further detail below with reference to examples.
First, 11 examples and 2 comparative examples were provided, and specific alloy compositions are shown in table 1, and were prepared as strip samples, respectively.
Taking the alloy of example 1 as an example, a strip sample was prepared, with the following preparation procedure: casting, hot rolling, rough rolling, primary aging heat treatment, intermediate rolling, secondary aging heat treatment and finish rolling, and specifically comprises the following steps:
proportioning according to the required components, smelting by adopting an induction furnace, wherein the smelting and casting temperature is 1200 ℃, and casting ingots after detecting that the components meet the requirements and fully degassing and deslagging; carrying out hot rolling cogging after preserving the ingot for 3 hours at an initial temperature of 920 ℃, wherein the total processing rate of hot rolling is 95%; milling the surface of the strip after hot rolling treatment to remove the surface oxide film, and then performing rough rolling processing, wherein the total processing rate of rough rolling is 70%; carrying out primary aging heat treatment on the rough rolled strip at 500 ℃, and preserving heat for 6 hours; after the strip subjected to primary aging heat treatment is cleaned, middle rolling processing with the processing rate of 50 percent is applied; carrying out secondary aging heat treatment on the strip after the intermediate rolling, wherein the aging temperature and the heat preservation time are 400 ℃ and 6 hours respectively; after the secondary aging heat treatment, the strip was subjected to finish rolling, and the total processing rate of the finish rolling was 10%, to prepare a strip sample of example 1.
The following tests were performed on the strip samples of the examples and comparative examples:
tensile strength: according to GB/T228.1-2010 section 1 Metal tensile test: room temperature test method room temperature tensile test was performed on an electronic universal mechanical property tester at a tensile speed of 5mm/min.
Conductivity of: the conductivity of the strip samples was tested using the GB/T32791-2016 copper and copper alloy conductivity vortex test method.
Elongation in all directionsThe specificity: according to GB/T228.1-2010 section 1 Metal tensile test: room temperature test method measuring the elongation in the width and length directions of the sample, the elongation in the width direction being δ w Elongation in the longitudinal direction was δ l By delta w /δ l The ratio of the elongation in the width direction W to the elongation in the length direction L of the strip sample is calculated as a parameter of the elongation anisotropy.
Average grain size: after the samples are polished, the size of the crystal grains is observed by using a scanning electron microscope, 5 view fields are randomly collected for each sample, and the average value is calculated by measuring the size of the crystal grains by using electron microscope analysis software.
Precipitated phase particles containing O: the observation regions were randomly arranged in the field of view of the section of the strip sample by a transmission electron microscope, and the observation regions were rectangular at 400nm×250 nm. Five points are randomly taken from the copper matrix part in the observation area to carry out EDS analysis, and the detection intensity of the measured O element is averaged to be I a . Next, EDS analysis was performed under the same test conditions on particles having a different contrast from the copper matrix in the observation region to determine the above I a The number of the granular substances with the detection intensity of the O element more than 10 times is counted as A.
Texture: analysis of the texture type and area ratio of the strip samples by EBSD, wherein the area ratio of each orientation texture means the ratio of the area within 15 DEG of each orientation deviation angle divided by the measured area, {110}<112>The area ratio of the brass texture is S b ，{011}<100>The area ratio of the Gaussian texture is Sg, {112}, and<111>the area ratio of the copper texture is S c Calculate (S g +S b )/S c Values.
The microstructure and properties of the tape samples of examples 1 to 11 and comparative examples 1 to 2 are shown in Table 2. As can be seen from Table 2, the number A of O-containing precipitated phase particles in the microstructure of the strip samples of examples 1 to 11 was 5/. Mu.m or less 2 And the area ratio S of the Gaussian texture g Area ratio S of brass texture b And copper type textureThe area ratio S of (2) c Meets the requirement of 0.5 to less than or equal to S g +S b )/S c Less than or equal to 1.5; the strip samples of examples 1 to 11 had softening temperatures of 500℃or higher and elongation delta in the strip width direction w Elongation delta from length direction l Satisfy delta w /δ l Not less than 0.6, and can ensure good strength and cold processing performance while showing excellent high temperature resistance and good conductivity.
As a comparison, in comparative examples 1 and 2, the number of O-containing precipitated phase particles was too high, and the target value of the present invention was not fully attained in terms of strength, conductivity, softening temperature, elongation anisotropy, and the like.
Table 1: alloy compositions of examples 1 to 11 and comparative examples 1 to 2
Table 2: microstructure and Properties of the tape samples of examples 1-11 and comparative examples 1-2
*：{110}<112>The area ratio of the brass texture is S b ，{011}<100>The area ratio of the Gaussian texture is S g ，{112}<111>The area ratio of the copper texture is S c 。
Example 12: carrying out primary aging heat treatment on the rough rolled strip in the embodiment 3 at 450 ℃ and preserving heat for 6 hours; after the strip subjected to primary aging heat treatment is cleaned, middle rolling processing with the processing rate of 50 percent is applied; performing secondary aging heat treatment on the intermediate rolled strip, wherein the aging temperature and the heat preservation time are respectively 300 ℃ and 6 hours; after the secondary aging heat treatment, the strip was subjected to finish rolling, and the total processing rate of the finish rolling was 10%, to prepare a strip sample of example 12.
Example 13: the difference from example 12 is that the primary aging heat treatment in example 13 was carried out at 600℃for a holding time of 6 hours; the temperature of the secondary aging is 420 ℃, and the heat preservation time is 6 hours.
Comparative example 3: the difference from example 12 is that the primary aging heat treatment in comparative example 3 was carried out at 400℃for 6 hours; the temperature of the secondary aging is 500 ℃, and the heat preservation time is 6 hours.
Comparative example 4: the difference from example 12 is that the primary aging heat treatment in comparative example 4 was carried out at 500℃for 4 hours; the temperature of the secondary aging is 400 ℃, and the heat preservation time is 4 hours.
The microstructure and properties of the strip samples of example 3, example 12 to example 13 and comparative examples 3 to comparative example 4 are shown in Table 3. As can be seen from table 3, comparative examples 3 to 4 show a significant decrease in conductivity or elongation anisotropy due to the different aging processes.
Table 3: microstructure and properties of tape samples of example 3, example 12 to example 13 and comparative examples 3 to comparative example 4
Example 14: using the cast ingot in example 3, heat-preserving for 3 hours at an initial temperature of 880 ℃ and then hot-rolling and cogging, wherein the total processing rate of hot rolling is 95%; milling the surface of the strip after hot rolling treatment to remove the surface oxide film, and then performing rough rolling processing, wherein the total processing rate of rough rolling is 70%; carrying out primary aging heat treatment on the rough rolled strip at the temperature of 500 ℃, and preserving heat for 6 hours; after the strip subjected to primary aging heat treatment is cleaned, middle rolling processing with the processing rate of 50 percent is applied; performing secondary aging heat treatment on the intermediate rolled strip, wherein the aging temperature and the heat preservation time are 400 ℃ and 6 hours respectively; after the secondary aging heat treatment, the strip was subjected to finish rolling, and the total processing rate of the finish rolling was 10%, to prepare a strip sample of example 14.
Example 15: the difference from example 14 is that the initial temperature of rough rolling in example 15 was 980℃and the processing rate was 90%.
Comparative example 5: the difference from example 14 is that the initial temperature of rough rolling in comparative example 5 was 920℃and the working ratio was 70%.
The microstructure and properties of the strip samples of example 3, example 14 to example 15 and comparative example 5 are shown in Table 4. As can be seen from Table 4, comparative example 5 has a large difference in the ratio of texture in the microstructure of the produced strip from the low rough rolling reduction, and the anisotropy of elongation does not satisfy the requirement.
Table 4: microstructure and properties of the tape samples of example 3, example 14 to example 15 and comparative example 5
Example 16: after the strip subjected to the primary aging heat treatment in the above example 3 was cleaned, a middle rolling process was performed at a working rate of 30%; performing secondary aging heat treatment on the intermediate rolled strip, wherein the aging temperature and the heat preservation time are 400 ℃ and 6 hours respectively; after the secondary aging heat treatment, the strip was subjected to finish rolling, and the total processing rate of the finish rolling was 30%, to prepare a strip sample of example 16.
Comparative example 6: the difference from example 16 is that the working ratio of the intermediate rolling is 30% and the working ratio of the finish rolling is 50%.
Comparative example 7: the difference from example 16 is that the working ratio of the intermediate rolling is 50% and the working ratio of the finish rolling is 30%.
The microstructure and properties of the tape samples of example 3, example 6 and comparative examples 6 to 7 are shown in Table 5. As can be seen from Table 5, comparative examples 6 and 7 use a larger intermediate rolling or finish rolling ratio, the sum of which is larger than that of the rough rolling, and the electrical conductivity of the produced strip is drastically reduced, and the ratio of texture in the microstructure of the strip is greatly different from that of the present invention, and the anisotropy of elongation does not satisfy the requirements.
Table 5: microstructure and properties of tape samples of example 3, example 16 and comparative examples 6 to 7
Claims (6)
1. The copper-zirconium alloy plate strip is characterized by comprising the following components in percentage by mass: 0.05 to 0.5 weight percent of O: less than or equal to 10ppm, and the balance of Cu and unavoidable impurities; the number of the precipitated phase particles containing O is expressed as A, and A is less than or equal to 5/mu m on the section of the copper-zirconium alloy plate strip perpendicular to the rolling direction 2 The method comprises the steps of carrying out a first treatment on the surface of the The average grain size in the microstructure of the copper-zirconium alloy plate strip is less than or equal to 50 mu m; area ratio S of Gaussian texture in microstructure of copper-zirconium alloy plate strip g Area ratio S of brass texture b And the area ratio S of the copper texture c Meets the requirement of 0.5 to less than or equal to S g +S b ）/S c Less than or equal to 1.5; the tensile strength of the copper-zirconium alloy plate strip is above 350MPa, the conductivity is above 85% IACS, and the softening temperature is more than or equal to 500 ℃; the elongation percentage of the copper-zirconium alloy plate strip in the width direction is delta w Elongation in the longitudinal direction was δ l Both satisfy delta w /δ l ≥0.6。
2. The copper-zirconium alloy sheet strip according to claim 1, further comprising 0.01 to 1.0wt% of X in total, wherein X is at least one selected from Mg, cr, mn, si, ni, fe, B, P, RE.
3. A method for producing a copper-zirconium alloy sheet strip as claimed in any one of claims 1 to 2, comprising the following steps: casting, hot rolling, rough rolling, primary aging heat treatment, intermediate rolling, secondary aging heat treatment and finish rolling; the temperature of the primary aging heat treatment is 440-600 ℃, and the temperature of the secondary aging heat treatment is 300-440 ℃.
4. The method for producing a copper-zirconium alloy sheet strip according to claim 3, wherein the total holding time of the primary aging heat treatment and the secondary aging heat treatment is not less than 10 hours.
5. The method for producing a copper-zirconium alloy strip according to claim 3, wherein the initial temperature of the hot rolling is 880 to 1000 ℃ and the total working rate of the hot rolling is 90% or more.
6. The method of producing a copper-zirconium alloy strip as claimed in claim 3, wherein the total working ratio of the rough rolling is not less than the sum of the total working ratio of the intermediate rolling and the total working ratio of the finish rolling.
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