CN102286715A - Stabilization Heat Treatment Process of Deformed Zn-Al Alloy - Google Patents
Stabilization Heat Treatment Process of Deformed Zn-Al Alloy Download PDFInfo
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Abstract
本发明涉及变形Zn-Al合金的一种稳定化热处理方法，其工艺步骤如下：将材料或工件在电阻炉内加热至300～370℃，根据材料或工件大小，保温一定时间，随炉冷却至220～280℃，保温10～40min，再随炉冷却至70～150℃，保温6～16h，然后空冷至室温。本发明采用三重退火的稳定化热处理方法，可有效改善变形Zn-Al合金组织均匀性，提高了变形Zn-Al合金的尺寸稳定性和综合力学性能，工艺简单，可操作性强，生产效率高；并且解决了常规变形Zn-Al合金常规稳定化热处理方法耗时长、生产效率低、成本高等突出问题，为变形Zn-Al合金的产业化生产提供了坚实的理论基础和技术指导，是一种高效可行的热处理方法。
The invention relates to a stabilized heat treatment method for deformed Zn-Al alloys. The process steps are as follows: heat the material or workpiece to 300-370°C in a resistance furnace, keep it warm for a certain period of time according to the size of the material or workpiece, and cool it with the furnace to 220-280°C, keep warm for 10-40min, then cool to 70-150°C with the furnace, keep warm for 6-16h, then air-cool to room temperature. The invention adopts the stabilizing heat treatment method of triple annealing, which can effectively improve the microstructure uniformity of the deformed Zn-Al alloy, improve the dimensional stability and comprehensive mechanical properties of the deformed Zn-Al alloy, and has simple process, strong operability and high production efficiency ; and solve the conventional deformation Zn-Al alloy conventional stabilization heat treatment method takes a long time, low production efficiency, high cost and other outstanding problems, provides a solid theoretical basis and technical guidance for the industrial production of deformed Zn-Al alloy, is a kind of Efficient and feasible heat treatment method.
Description
Technical field
The present invention relates to be out of shape Zn-Al alloy stabilization thermal treatment process, belong to metallic substance heat treatment technics field.
Background technology
In non-ferrous metal, the reserves of zinc, output and consumption are only second to aluminium and copper, occupy the 3rd.China has more rich zinc resource, but in the structured material field, the ratio of zinc and zinc alloy is also quite low, and this mainly is because China is comparatively weak to the fundamental research of deformation zinc alloy and application facet thereof.Zinc alloy is to be that matrix adds the non-ferrous alloy material that other elements are produced with zinc, has advantages such as fusing point is low, good casting property, mechanical property excellence, the technological process of production is short, energy consumption is little, starting material are cheap and easy to get, has wide Application Areas.Especially now along with the day of copper resource is becoming tight, technology such as " with zinc for copper ", " with zinc joint copper " becomes the research and development direction that state key is supported, so at present both at home and abroad the research for zinc alloy becomes focus gradually, zinc alloy even be described as the novel material of 21st century.
Though deformation zinc alloy is restricted aspect process velocity, but it is poor day by day in the copper resource, in the time of price increase, research and develop out the deformation zinc alloy that substitutes the copper alloy of expensive poorness in suitable field, be subjected to the attention of more and more material supplier authors and industrial community.In recent years, Chinese scholars has been carried out the development of high-strength deformation Zn-Al alloy and the research of aspects such as thermal treatment, surface treatment and welding technique, and has obtained certain achievement in research.
Through the development of decades, deformation zinc alloy research at home and abroad is increasingly extensive with application.Deformation zinc alloy can be divided into rolled zinc alloy, extruded zinc alloy and drawing zinc alloy according to working method.Rolling zinc and zinc alloy can be divided into Zn, Zn-Cu, Zn-Cu-Ti, Zn-Pb-Cd and Zn-Al alloy by composition, are mainly used in battery zine plate, building and decorate roof boarding, damping device etc.; Extruding zinc and zinc alloy can be divided into Zn, Zn-Al, Zn-Cu-Ti, Zn-Mg, Zn-Al-Cu-Mn etc. by composition, as sacrificial anode material, turbine, axle sleeve, nut, household, hot-water heating, stationery, slide fastener etc.; The drawing zinc alloy is mainly Zn-Al alloy, make line, rod by drawing deformation after, mainly as thermospray metal wire, welding material, and system nail, screw, net etc.
The distortion Zn-Al alloy in use exists a fatal shortcoming---" wearing out ", mainly shows the size instability, reduces the work-ing life of material greatly, and its application in many occasions all is restricted.General distortion Zn-Al alloy parts all are directly to use behind extruding attitude or common annealing, and the phenomenon that swells of size can take place in the use.The reason that swells is to be caused by corrosion on the one hand, is caused by phase transformation exactly on the other hand.
The distortion Zn-Al alloy has just contained Cu since coming out, because Cu not only has strengthening effect to the Zn alloy, and can also improve the anti intercrystalline corrosion ability of alloy greatly, improves the solidity to corrosion of Zn alloy.But the adding of Cu has increased the dimensional instability of alloy, and the Zn alloy that contains Cu has bigger contraction at first in ag(e)ing process, the marked inflation phenomenon is arranged again subsequently.Four phase reactions in the alloy Natural Aging Process: the phase transition process such as precipitation of the precipitation of α+ε → T '+β, rich aluminium α phase, the volume effect of eutectoid reaction β → α+η, rich zinc η phase all can cause distortion Zn-Al alloy size pucker ﹠ bloat in various degree.
Therefore, the distortion Zn-Al alloy is carried out stabilization thermal treatment, be farthest to eliminate uneven phase in the alloy, promote four phase reactions of ε phase (CuZn4) and the precipitation of supersaturated solid solution to decompose, reduce the gordian technique of the dimensional change that causes by phase transformation in material or the workpiece use.
Experiment shows that the stabilization thermal treatment process of zinc alloy routine is the long-time ageing treatment of low temperature, and the alloy size just tends towards stability after insulation 100h under 100 ℃.Sun Lianchao pointed out once also in " zinc and zinc alloy physical metallurgy " that the Zn-10Al-5Cu-0.55Mg alloy after through 350 ℃ of shrend+150 ℃ timeliness 50h, can weaken the size bulking effect in the use greatly.But these two kinds of thermal treatment process length consuming time, explained hereafter cost height, energy consumption height, efficient are slow.
Up to now, the relevant patent report of Shang Weiyou distortion Zn-Al alloy stabilization thermal treatment process does not more have its weak point consuming time, stabilization thermal treatment public technology report that efficient is high.
Summary of the invention
The objective of the invention is to overcome the deficiency of prior art and provide that a kind of processing method is simple, easy to operate, process cycle is short, energy consumption is low, the distortion Zn-Al alloy homogeneous microstructure after handling, dimensional stabilizing, comprehensive mechanical property be improved significantly distortion Zn-Al alloy stabilization thermal treatment process.
The present invention is out of shape Zn-Al alloy stabilization thermal treatment process, comprises the steps:
The first step: high temperature annealing
Material or workpiece are heated to 330～370 ℃ of insulations, and soaking time is determined according to material or workpiece size;
Second step: medium annealing
Cool to the material or the workpiece of the first step heating with the furnace 220～280 ℃, insulation 10～40min;
The 3rd step: low-temperature annealing
Cool to the material or the workpiece of the heating of second step with the furnace 70～150 ℃, insulation 6～16h, air cooling is to room temperature again.
The present invention is out of shape in the Zn-Al alloy stabilization thermal treatment process, and the soaking time of described high temperature annealing is:: cylindrical material or workpiece, by every mm dia insulation 0.8～1.4min; Square material or workpiece are by every millimeter thickness insulation 1.6～2.2min; Flat-form material or workpiece, by every millimeter thickness insulation 2.4～3.0min, described flat-form material is flakiness ratio 〉=5; Square material is flakiness ratio＜5.
The present invention is out of shape in the Zn-Al alloy stabilization thermal treatment process, in the described Zn-Al alloy, by weight percentage, aluminium content is 5-15%, copper content is 1.5～5%, simultaneously, contains at least a alloying element in magnesium, titanium, bismuth, the tin, surplus is zinc and unavoidable impurities, foreign matter content≤0.15%; Described magnesium, titanium, bismuth, the total weight percent of tin alloy element are 0.02～2%.
The present invention is owing to adopt aforementioned stable heat-transmission treatment process, utilize triple annealing technology, effectively eliminated uneven phase in the alloy, alloy dimensional stability and comprehensive mechanical property have been improved, using for the following process of material provides higher accuracy guarantee, and its mechanism that produces above-mentioned advantage is summarized as follows:
Distortion Zn-Al alloy homogeneous microstructure and very tiny after extruding, rolling or drawing, mainly comprise rich zinc η phase, α+η synusia shape, born of the same parents' shape and granular structure, non-equilibrium β (ZnAl) phase, wherein η is rich Zn phase mutually, and α is rich Al phase mutually, and β is the ZnAl phase mutually.Alloy is in the room temperature Natural Aging Process, and non-equilibrium β (ZnAl) is mutually with the spontaneous α+η synusia shape tissue that resolves into, and the difference of the lattice parameter of each phase causes the volume of alloy to shrink before and after decomposing; There is ε phase (CuZn in the Zn-Al alloy alloy of interpolation copper
4), this phase participates in α+ε → T '+β four phase reactions at normal temperatures, causes the expansion largely of volume; The precipitation decomposition at normal temperatures of supersaturation α, η sosoloid also is the important factor that causes distortion Zn-Al alloy dimensional change in the alloy.Considerable change has taken place through the heat treated distortion Zn-Al alloy of triple annealing stabilization tissue, 330～370 ℃ high temperature annealing has improved the solid solubility of Cu element in the alloy, improved the intensity and the hardness of material, promoted separating out of ε phase simultaneously, for four follow-up phase reactions lay the foundation; Eutectoid reaction has taken place in non-equilibrium β (ZnAl) mutually in the medium annealing stage alloy, makes the non-equilibrium β in the alloy that sufficient decomposition take place mutually, generates α+η synusia shape tissue, improves homogeneity of structure; ε in the alloy obviously reduces mutually after low-temperature annealing is handled again, α+η born of the same parents' shape and granular structure significantly increase, show that the precipitation decomposition of above-mentioned four phase reactions and supersaturated solid solution only takes place Zn-Al alloy in the low-temperature annealing process, it is uniform and stable that alloy organizing just can be tending towards, and the intensity of alloy and hardness have raising slightly, unit elongation significantly improves, and comprehensive mechanical property and dimensional stability are greatly improved.
The present invention is out of shape the stabilization thermal treatment process of Zn-Al alloy and passes through verification experimental verification, determined soaking time, especially the optimum value of high temperature annealing time, hot stage Heating temperature and soaking time realize quantitatively complementary, thereby farthest shorten the soaking time of whole thermal treatment process, on the basis of improving alloy dimensional stability and comprehensive mechanical property, enhance productivity, reduce cost.
The present invention compares with conventional art, has following superiority:
(1) the stabilization heat-treatment technology method of distortion Zn-Al alloy provided by the invention is simple, easy to operate.
(2) the stabilization thermal treatment process soaking time of distortion Zn-Al alloy provided by the invention is short, than the traditional time of stabilizing heat treatment method shortening more than 70%, has improved production efficiency greatly, reduces cost.
(3) the distortion Zn-Al alloy dimensional stability after the stabilization thermal treatment provided by the invention is better, guaranteed alloy dimensional precision preferably, has broken the constraint that zinc alloy can not be used in the fine structure part, can open up the new application of deformation zinc alloy.
(4) distortion Zn-Al alloy intensity and the plasticity after the stabilization thermal treatment provided by the invention is all higher, processes basis and use properties preferably for the following process of alloy and use provide.
In sum, the present invention adopts the stabilizing heat treatment method of triple annealing, has improved the dimensional stability and the comprehensive mechanical property of distortion Zn-Al alloy, and technology is simple, and is workable, the production efficiency height; And outstanding problems such as the conventional stabilizing heat treatment method of conventional distortion Zn-Al alloy length consuming time, production efficiency are low, cost height have been solved, for the industrialization production of being out of shape Zn-Al alloy provides solid theory and technical director, be a kind of efficient feasible heat treating method.
Description of drawings
Accompanying drawing 1 is the not stabilized heat treated distortion Zn-Al alloy extruding attitude SEM photo of comparison example.
Accompanying drawing 2 is the embodiment of the invention 1 a stabilization thermal treatment after strain Zn-Al alloy SEM photo.
Accompanying drawing 3 is the embodiment of the invention 2 stabilization thermal treatment after strain Zn-Al alloy SEM photos.
Accompanying drawing 4 is the embodiment of the invention 3 stabilization thermal treatment after strain Zn-Al alloy SEM photos.
Accompanying drawing 5 is the embodiment of the invention 4 stabilization thermal treatment after strain Zn-Al alloy SEM photos.
Accompanying drawing 6 is the embodiment of the invention 5 stabilization thermal treatment after strain Zn-Al alloy SEM photos.
Accompanying drawing 7 is a sample pliability test pictorial diagram before and after the embodiment of the invention 6 stabilization thermal treatments.
Accompanying drawing is non-limiting to disclose concrete embodiment of the present invention, and the invention will be further described below in conjunction with figure.
Comparative Examples:
With starting material such as zinc, aluminium, copper, magnesium, titanium, bismuths, by following weight percent melting: Al 10% in the dissolving stove; Cu 2.5%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other are zinc and unavoidable impurities (foreign matter content≤0.15%).Be squeezed into the bar that diameter is 15mm after the founding; Alloy to the extruding attitude carries out structure observation and Mechanics Performance Testing, and referring to Fig. 1, distortion Zn-10Al alloy structure exists rich zinc η phase, α+η synusia shape, born of the same parents' shape and granular structure, ε phase and non-equilibrium black β (ZnAl) mutually.Mechanical performance index sees Table 1.
Embodiment 1:
With composition is Al 10%; Cu 2.5%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other distortion Zn-Al alloy extruding rods for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 360 ℃ with the stove intensification, insulation 20min, cool to 260 ℃ then with the furnace, be incubated 10min again, cool to 140 ℃ again with the furnace, insulation 8h, air cooling is to room temperature.Alloy after the thermal treatment is carried out microstructure analysis and Mechanics Performance Testing, referring to accompanying drawing 2, compare with Comparative Examples, in the distortion Zn-10Al alloy structure after the thermal treatment of this embodiment stabilization, non-equilibrium β (ZnAl) disappears mutually substantially, rich copper ε phase basically eliminate.Alloy mechanical property index after the thermal treatment of present embodiment stabilization sees Table 1.
Embodiment 2:
With composition is Al 10%; Cu 1.5%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other distortion Zn-Al alloy extruding rods for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 340 ℃ with the stove intensification, insulation 30min, cool to 225 ℃ then with the furnace, be incubated 20min again, cool to 90 ℃ again with the furnace, insulation 14h, air cooling is to room temperature.Alloy after the thermal treatment is carried out microstructure analysis and Mechanics Performance Testing, referring to accompanying drawing 3, compare with Comparative Examples, in the distortion Zn-10Al alloy structure after the thermal treatment of this embodiment stabilization, eutectoid reaction has taken place is transformed into α+η synusia shape, born of the same parents' shape and granular structure to non-equilibrium β (ZnAl) mutually, and rich copper ε reduces mutually to some extent.Alloy mechanical property index after the thermal treatment of present embodiment stabilization sees Table 1.
Embodiment 3:
With composition is Al 10%; Cu 2.5%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other distortion Zn-Al alloy extruding groups for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 350 ℃ with the stove intensification, insulation 25min, cool to 240 ℃ then with the furnace, be incubated 15min again, cool to 120 ℃ again with the furnace, insulation 10h, air cooling is to room temperature.Alloy after the thermal treatment is carried out microstructure analysis and Mechanics Performance Testing, referring to accompanying drawing 4, compare with the tissue of embodiment 1, organize considerable change does not take place, from the actual production angle, it is unnecessary prolonging the low-temperature annealing soaking time.Alloy mechanical property index after the thermal treatment of present embodiment stabilization sees Table 1.
Embodiment 4:
With composition is Al 5%; Cu 3.0%; Ti 0.3%; Bi 0.05%; All the other distortion Zn-Al alloy extruding rods for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 350 ℃ with the stove intensification, insulation 24min, cool to 250 ℃ then with the furnace, be incubated 13min again, cool to 120 ℃ again with the furnace, insulation 10h, air cooling is to room temperature.Alloy after the thermal treatment is carried out microstructure analysis and Mechanics Performance Testing, and referring to accompanying drawing 5, in the distortion Zn-8Al alloy structure after the thermal treatment of this embodiment stabilization, non-equilibrium black β (ZnAl) disappears mutually substantially, rich copper ε phase basically eliminate.Alloy mechanical property index after the thermal treatment of present embodiment stabilization sees Table 1.
Embodiment 5:
With composition is Al 15%; Cu 3.5%; Mg 0.02%, and Bi 0.02%, and Sn 0.01; All the other distortion Zn-Al alloy extruding rods for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 340 ℃ with the stove intensification, insulation 28min, cool to 225 ℃ then with the furnace, be incubated 20min again, cool to 100 ℃ again with the furnace, insulation 12h, air cooling is to room temperature.Alloy after the thermal treatment is carried out microstructure analysis and Mechanics Performance Testing, referring to accompanying drawing 6, compare with Comparative Examples, in the distortion Zn-15Al alloy structure after the thermal treatment of this embodiment stabilization, eutectoid reaction has taken place is transformed into α+η synusia shape, born of the same parents' shape and granular structure to non-equilibrium β (ZnAl) mutually, and rich copper ε reduces mutually to some extent.Alloy mechanical property index after the thermal treatment of present embodiment stabilization sees Table 1.
Embodiment 6:
With composition is Al 10%; Cu 3.0%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other distortion Zn-Al alloy extruding groups for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 350 ℃ with the stove intensification, insulation 25min, cool to 240 ℃ then with the furnace, be incubated 15min again, cool to 120 ℃ again with the furnace, insulation 10h is chilled to room temperature with stove.It is 6mm pole sample that stores van before and after the thermal treatment is processed into diameter, sample center loaded 5MPa power is carried out the simply supported beam pliability test, take off after 10 days, bending has in various degree all taken place in sample, carry out the Calculation of Deflection contrast after the measurement, not stabilized heat treated sample amount of deflection is 1.974mm, and the sample amount of deflection after the stabilization thermal treatment is 1.322mm, promptly after triple annealing stabilization provided by the invention thermal treatment, the alloy dimensional stability has improved 33.03%.Sample pliability test macro morphology after the thermal treatment of present embodiment stabilization is seen Fig. 7.
Embodiment 7:
With composition is Al 10%; Cu 5.0%; Ti 0.5%; Mg 0.02%, and Bi 0.03%; All the other distortion Zn-Al alloy extruding groups for zinc and unavoidable impurities (foreign matter content≤0.15%) carry out stabilization thermal treatment in resistance furnace, be heated to 350 ℃ with the stove intensification, insulation 25min, cool to 240 ℃ then with the furnace, be incubated 15min again, cool to 120 ℃ again with the furnace, insulation 10h is chilled to room temperature with stove.Material before and after the thermal treatment is become the tensile creep sample by GB/T 2039-1997 Vehicle Processing, the power that loads 5MPa on creep testing machine is carried out the constant load tension test, take off sample after 10 days and measure contrast, not stabilized heat treated specimen size creep compliance is 1.065%, specimen size creep compliance after the stabilization thermal treatment is 0.663%, promptly after triple annealing stabilization provided by the invention thermal treatment, the alloy dimensional stability has improved 37.75%.
The mechanical property of table 1 embodiment and comparison example
The result of table 1 shows, the tissue of embodiment 1, embodiment 2, embodiment 3, embodiment 4 and embodiment 5 and mechanical property are all comparatively desirable, the distortion Zn-Al alloy is at 300～370 ℃ of insulation certain hours, cool to 220～280 ℃ with the furnace, insulation 10～40min cools to 70～150 ℃ again with the furnace, insulation 6～16h, air cooling can significantly improve alloy structure homogeneity and stability to room temperature then, improves alloy alloy dimensional stability and comprehensive mechanical property largely.But the thermal treatment soaking time of embodiment 3 is all longer than other embodiments, and from the actual production angle, what prolong the low-temperature annealing time is unnecessary.
The invention provides the thinking and the method for distortion Zn-Al alloy stabilization thermal treatment process.The foregoing description is used for explaining the present invention, rather than limits the invention, and under the prerequisite that does not break away from the principle of the invention, can also make some improvements and modifications, and these improvements and modifications also are considered as protection scope of the present invention.
Claims (3)
1. distortion Zn-Al alloy stabilization thermal treatment process comprises the steps:
The first step: high temperature annealing
Material or workpiece are heated to 330～370 ℃ of insulations, and soaking time is determined according to material or workpiece size;
Second step: medium annealing
Cool to the material or the workpiece of the first step heating with the furnace 220～280 ℃, insulation 10～40min;
The 3rd step: low-temperature annealing
Cool to the material or the workpiece of the heating of second step with the furnace 70～150 ℃, insulation 6～16h, air cooling is to room temperature again.
2. distortion Zn-Al alloy stabilization thermal treatment process according to claim 1, it is characterized in that: the soaking time of described high temperature annealing is:: cylindrical material or workpiece, by every mm dia insulation 0.8～1.4min; Square material or workpiece are by every millimeter thickness insulation 1.6～2.2min; Flat-form material or workpiece are by every millimeter thickness insulation 2.4～3.0min.
3. distortion Zn-Al alloy stabilization thermal treatment process according to claim 2, it is characterized in that: in the described Zn-Al alloy, by weight percentage, aluminium content is 5～15%, copper content is 1.5～5%, simultaneously, contains at least a alloying element in magnesium, titanium, bismuth, the tin, surplus is zinc and unavoidable impurities, foreign matter content≤0.15%; Described magnesium, titanium, bismuth, the total weight percent of tin alloy element are 0.02～2%.
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| CN 201110265921 CN102286715B (en) | 2011-09-08 | 2011-09-08 | Stabilization Heat Treatment Process of Deformed Zn-Al Alloy |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851475A (en) * | 2012-08-31 | 2013-01-02 | 绍兴文理学院 | Manufacturing process for zinc-aluminum alloy wire |
| CN103924179A (en) * | 2014-03-28 | 2014-07-16 | 上海龙烁焊材有限公司 | Heat treatment method of zinc-aluminum rolled strip |
| CN110349722A (en) * | 2019-07-12 | 2019-10-18 | 南京萨特科技发展有限公司 | A kind of heat treatment method of alloy fled rheostat |
| CN115343275A (en) * | 2022-08-02 | 2022-11-15 | 苏州市祥冠合金研究院有限公司 | YZZnAl 4 Cu 1 Preparation method of spectral standard sample |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3734785A (en) * | 1969-12-31 | 1973-05-22 | Cominco Ltd | Zinc forging alloy |
| CN1974811A (en) * | 2006-12-06 | 2007-06-06 | 宁波博威集团有限公司 | Process of making zinc-base alloy wire and rod with high strength and high toughness |
-
2011
- 2011-09-08 CN CN 201110265921 patent/CN102286715B/en not_active Expired - Fee Related
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US3734785A (en) * | 1969-12-31 | 1973-05-22 | Cominco Ltd | Zinc forging alloy |
| CN1974811A (en) * | 2006-12-06 | 2007-06-06 | 宁波博威集团有限公司 | Process of making zinc-base alloy wire and rod with high strength and high toughness |
Non-Patent Citations (1)
| Title |
|---|
| A. ABU ARAB ET AL.: "THE STABILIZATION OF MARTENSITE IN Cu-Zn-Al ALLOYS", 《ACTA METALL.》, vol. 36, no. 9, 31 December 1988 (1988-12-31), pages 2627 - 2638 * |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102851475A (en) * | 2012-08-31 | 2013-01-02 | 绍兴文理学院 | Manufacturing process for zinc-aluminum alloy wire |
| CN103924179A (en) * | 2014-03-28 | 2014-07-16 | 上海龙烁焊材有限公司 | Heat treatment method of zinc-aluminum rolled strip |
| CN110349722A (en) * | 2019-07-12 | 2019-10-18 | 南京萨特科技发展有限公司 | A kind of heat treatment method of alloy fled rheostat |
| CN110349722B (en) * | 2019-07-12 | 2021-04-30 | 南京萨特科技发展有限公司 | Heat treatment method of alloy resistor |
| CN115343275A (en) * | 2022-08-02 | 2022-11-15 | 苏州市祥冠合金研究院有限公司 | YZZnAl 4 Cu 1 Preparation method of spectral standard sample |
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| CN102286715B (en) | 2013-01-30 |
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