CN103310914B - A kind of high-strength MgB 2the preparation method of wire rod - Google Patents
A kind of high-strength MgB 2the preparation method of wire rod Download PDFInfo
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- CN103310914B CN103310914B CN201310275468.7A CN201310275468A CN103310914B CN 103310914 B CN103310914 B CN 103310914B CN 201310275468 A CN201310275468 A CN 201310275468A CN 103310914 B CN103310914 B CN 103310914B
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Abstract
The invention discloses a kind of high-strength MgB
2the preparation method of wire rod, the method is: one, prepare once-combined wire rod; Two, secondary multiple tube is assembled; Three, with 20% ~ 25% pass reduction to secondary multiple tube drawing 3 times, be then drawn to required size with the pass reduction of 10% ~ 15%, obtain wire rod; Four, wire rod is carried out into phase heat treatment under argon gas atmosphere protection, obtain the high-strength MgB that intensity is 220MPa ~ 280MPa
2wire rod.The present invention adopts CuAg alloy bar as enhancing core, and evenly, inner each position combines closely, and has good plasticity because of it, being flowing in drawing process of powder can be made unblocked, be particularly suitable for MgB in the multi-core superconducting wire rod distortion of preparation
2the processing of km level long line, can meet the practical application of the superconducting magnet particularly aspect such as NMR spectrometer with superconducting magnet.
Description
Technical field
The invention belongs to superconductor processing engineering technology field, be specifically related to a kind of high-strength MgB
2the preparation method of wire rod.
Background technology
MgB
2critical transition temperature be 39k, there is higher superconducting transition temperature in metallic compound, can work at liquid hydrogen warm area (10-20k), and traditional cryogenic superconductor cannot realize application at this warm area, must use expensive liquid helium, this makes application cost strengthen.Found by years of researches, MgB
2can prepare wire rod, band in different ways, as in-situ method (in-situ) PIT and first position method (ex-situ) PIT technology, two kinds of technology can prepare the long line of km level.ASG, Columbus, Paramed in 2007 tri-open MgB of using of the refrigeration machine warm area of company's joint research and development
2-MRI superconducting magnet, is just the use of the MgB more than 1000 meters
2superconducting line strips, indication MgB
2there is good application prospect.
Compared with becoming a useful person with the PIT method of Bi series superconducting material, MgB
2become a useful person and there is its particularity, in above-mentioned two kinds of technologies of preparing, ex-situPIT law technology in preparation process, due to MgB
2hardness comparatively large, there is no the glide lamella etc. of similar Bi system, the micro-crack formed in mechanical processing process not only cannot be made up in follow-up magnet preparation process, also can be more serious.Therefore, ex-situPIT method cannot prepare practical MgB
2wire strip.In-situPIT method is the main flow direction of current Overseas Development, preparation method is loading in composite metal pipe after Mg powder and the grinding evenly of B powder, through swaging, the processes such as drawing and rolling is to certain specification size, last heat treatment at a certain temperature makes Mg, B become phase, inner superconducting core silk, due to the fusion of liquid phase magnesium, makes MgB
2have good connection between crystal grain, the gross imperfections such as crackle greatly reduce, and easily doping are incorporated in front axle shell the characteristic improving electric current degradation in magnetic field, finally can obtain the high MgB of current-carrying performance
2wire strip.MgB
2the field being hopeful most to apply is MRI magnet, and magnet preparation is higher to the mechanical property requirements of wire rod, due to MgB
2there is the fragility of class pottery, although in-situ method first processes to become phase afterwards, but still need the connectivity that sufficiently high intensity had to protect its intercrystalline.Its mechanical performance is mainly from four kinds of materials: one, basis material (Cu); Two, barrier layer metal (Nb); Three, the introducing of core is strengthened; Four, different core table structure, change the volume ratio of above-mentioned material and superconducting core silk, final wire rod macro-mechanical performance will follow law of mixtures.Find in research in the past, the wire strip of multicore structure (7,19,37 cores etc.) has larger difference due to the plasticity of plasticity and copper stabilized zone that center strengthens core CuNb, can not well synchronously extend in the drawing course of processing, cause the stress in wire rod centre excessive, finally make enhancing core place, superconducting core nearly center different with the distortion thickness at nearly outer jacket basis material Cu place, easily break when pulling to small size (< 2.0mm) core.Therefore, the mechanical strength improving wire strip of adopting an effective measure is very necessary.
Summary of the invention
Technical problem to be solved by this invention is for above-mentioned the deficiencies in the prior art, provides a kind of high-strength MgB
2the preparation method of wire rod.The method adopts CuAg alloy bar as enhancing core, Ag core silk in CuAg alloy bar has nanoscale, Ag continuous nano-fibre containing more than one hundred million core, ensure that CuAg alloy bar not only has close to the intensity of CuNb but also plasticity more than CuNb, close with the plasticity of liptinite copper, therefore prepared multi-core superconducting wire rod distortion evenly, inner each position combines closely, and because of it, there is good plasticity, being flowing in drawing process of powder can be made unblocked, be particularly suitable for MgB
2the processing of km level long line, can meet the practical application of the superconducting magnet particularly aspect such as NMR spectrometer with superconducting magnet (MRI).
For solving the problems of the technologies described above, the technical solution used in the present invention is: a kind of high-strength MgB
2the preparation method of wire rod, is characterized in that, the method comprises the following steps:
Step one, by amorphous boron powder, magnesium powder and doping powder according to 1: the atomic ratio of (2-x): x batching, under argon gas atmosphere protection ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, with the pass reduction drawing of 10% ~ 15%, obtaining cross section is circular once-combined wire rod, or cross section is orthohexagonal once-combined wire rod; Described doping powder is amorphous carbon or carbide; Described x is 0.05 ~ 0.15;
Step 2, once-combined wire rod described in 1 CuAg alloy bar and 6 steps one is placed in oxygen-free copper pipe assembles, obtain secondary multiple tube; Or once-combined wire rod described in 1 CuAg alloy bar, 6 steps one and 6 the 2nd CuAg alloy bars are placed in oxygen-free copper pipe assemble, obtain secondary multiple tube; A described CuAg alloy bar is positioned at oxygen-free copper pipe center, and once-combined wire rod loads in oxygen-free copper pipe around a CuAg alloy bar; In the space of described 2nd CuAg alloy bar between adjacent two once-combined wire rods and oxygen-free copper pipe;
Step 3, pass reduction with 20% ~ 25%, to the multiple tube of secondary described in step 2 drawing 3 times, are then drawn to required size with the pass reduction of 10% ~ 15%, obtain wire rod;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 220MPa ~ 280MPa
2wire rod.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, the quality purity of argon gas described in step one is 99.999%.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, in Precursor Powder described in step one, the mass percentage of oxygen is not more than 0.1%.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, diameter circular described in step one is 3.56mm ~ 8.6mm; Orthohexagonal inscribed circle diameter described in step one is 3.56mm ~ 8.6mm.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, carbide described in step one is titanium carbide.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, in the multiple tube of Nb/Cu described in step one, Nb is as inner barrier layer, and Cu is as outer liptinite.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, in a CuAg alloy bar described in step 2 and the 2nd CuAg alloy bar, the volumn concentration of Ag is 18% ~ 24%, and surplus is Cu.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, described in step 2, the size of a CuAg alloy bar is identical with once-combined wire size.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, the residual resistance ratio RRR of oxygen-free copper pipe described in step 2 is not less than 100.
The high-strength MgB of above-mentioned one
2the preparation method of wire rod, become mutually heat treated temperature to be 650 DEG C ~ 800 DEG C described in step 4, the time is 2h.
The present invention compared with prior art has the following advantages:
1, the present invention adopts CuAg alloy bar as enhancing core, Ag core silk in CuAg alloy bar has nanoscale, Ag continuous nano-fibre containing more than one hundred million core, ensure that CuAg alloy bar not only has close to the intensity of CuNb but also plasticity more than CuNb, close with the plasticity of liptinite copper, therefore prepared multi-core superconducting wire rod distortion evenly, inner each position combines closely, and because of it, there is good plasticity, being flowing in drawing process of powder can be made unblocked, be particularly suitable for MgB
2the processing of km level long line, can meet the practical application of the superconducting magnet particularly aspect such as NMR spectrometer with superconducting magnet (MRI).
2, the present invention passes through to MgB
2introduce the higher CuAg alloy bar of intensity (CuAg tensile strength is greater than 700MPa, and CuNb tensile strength is 400MPa ~ 700MPa) in wire rod, make superconducting core silk in drawing process have good intensity to ensure; In addition, can make the split conductor after heat treatment, plasticity is replied fast, when the disturbance of environment occurs wire rod in application process, is also conducive to the release postponing wire rod mechanical energy, reaches the continuous of protection wire internal superconducting core silk, ensures the stability of magnet system.
3, the present invention adopts CuAg alloy bar, and the nanometer Ag fiber in CuAg alloy bar has more interface, not only has higher intensity, and has good heat conductivity, can reduce the generation of joule heating effect.
4, MgB
2wire rod is when finished heat treatment, and the oxygen in Precursor Powder, hydrogen or carbon impurity are very large on the impact of niobium, and often a few millionths hundred, just can make its embrittlement.Consider as high-performance, the carbon that often will add chanza in Precursor Powder improves MgB
2transmission performance under High-Field, CuNb, as strengthening core, just very just carves the requirement of Precursor Powder, otherwise center booster action will be caused to weaken even destroy, thus affects being uniformly distributed of wire rod inner core silk, and multi-core conductor structural homogeneity is affected.And the CuAg alloy bar that the present invention adopts, avoid the shortcoming of above-mentioned CuNb, not by the impact of Precursor Powder composition, can ensure that inner core silk is uniformly distributed, thus improve the mechanical strength of wire rod when practical application.
5, the present invention by arranging CuAg alloy bar in the space between adjacent two once-combined wire rods and oxygen-free copper pipe, better ensure that the uniformity of superconducting core silk drawing deformation, the MgB of preparation
2wire rod is than the MgB not arranging CuAg alloy bar in space
2wire strength is higher.
Below in conjunction with drawings and Examples, technical scheme of the present invention is described in further detail.
Accompanying drawing explanation
The structural representation that Fig. 1 is the embodiment of the present invention 1, embodiment 7 and embodiment 9 assemble the secondary compound bar obtained.
The structural representation that Fig. 2 is the embodiment of the present invention 2, embodiment 8 and embodiment 10 assemble the secondary compound bar obtained.
The structural representation that Fig. 3 is the embodiment of the present invention 3, embodiment 5 and embodiment 11 assemble the secondary compound bar obtained.
The structural representation that Fig. 4 is the embodiment of the present invention 4, embodiment 6 and embodiment 12 assemble the secondary compound bar obtained.
Description of reference numerals:
1-once-combined wire rod; 2-the one CuAg alloy bar; 3-oxygen-free copper pipe;
4-the two CuAg alloy bar.
Embodiment
Embodiment 1
Step one, by amorphous boron powder, magnesium powder and amorphous carbon according to 1: 1.95: 0.05 atomic ratio batching, under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 10%, obtain the orthohexagonal once-combined wire rod that cross section is inscribed circle diameter 3.56mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 1, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 18%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 25% to the multiple tube of secondary described in step 2 drawing 3 times, then with 10% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 3mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 260MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 650 DEG C, and the time is 2h.
Embodiment 2
The present embodiment is identical with embodiment 1, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 2, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 0.89mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 18%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 280MPa.
Embodiment 3
Step one, by amorphous boron powder, magnesium powder and amorphous carbon according to 1: 1.95: 0.05 atomic ratio batching, under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 15%, obtain the once-combined wire rod that cross section is the circle of diameter 3.56mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 3, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 20%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 20% to the multiple tube of secondary described in step 2 drawing 3 times, then with 15% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 3mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 240MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 700 DEG C, and the time is 2h.
Embodiment 4
The present embodiment is identical with embodiment 3, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 4, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 0.89mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 20%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 260MPa.
Embodiment 5
Step one, by amorphous boron powder, magnesium powder and titanium carbide according to 1: 1.92: 0.08 atomic ratio batching (wherein titanium carbide is in the atomicity sum of carbon and titanium), under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 13%, obtain the once-combined wire rod that cross section is the circle of diameter 8.6mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 3, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 18%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 22% to the multiple tube of secondary described in step 2 drawing 3 times, then with 10% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 2mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 220MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 800 DEG C, and the time is 2h.
Embodiment 6
The present embodiment is identical with embodiment 5, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 4, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 2.15mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 20%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 240MPa.
Embodiment 7
Step one, by amorphous boron powder, magnesium powder and titanium carbide according to 1: 1.90: 0.1 atomic ratio batching (wherein titanium carbide is in the atomicity sum of carbon and titanium), under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 12%, obtain the orthohexagonal once-combined wire rod that cross section is inscribed circle diameter 8.6mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 1, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 22%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 22% to the multiple tube of secondary described in step 2 drawing 3 times, then with 12% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 3mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 230MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 750 DEG C, and the time is 2h.
Embodiment 8
The present embodiment is identical with embodiment 7, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 2, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 2.15mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 22%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 250MPa.
Embodiment 9
Step one, by amorphous boron powder, magnesium powder and titanium carbide according to 1: 1.85: 0.15 atomic ratio batching (wherein titanium carbide is in the atomicity sum of carbon and titanium), under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 15%, obtain the orthohexagonal once-combined wire rod that cross section is inscribed circle diameter 5.2mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 1, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 24%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 20% to the multiple tube of secondary described in step 2 drawing 3 times, then with 15% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 1mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 220MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 800 DEG C, and the time is 2h.
Embodiment 10
The present embodiment is identical with embodiment 9, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 2, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 1.3mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 24%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 230MPa.
Embodiment 11
Step one, by amorphous boron powder, magnesium powder and amorphous carbon according to 1: 1.92: 0.15 atomic ratio batching, under the argon gas atmosphere protection that quality purity is 99.999% ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, multiple tube one is screwed with cotton shutoff multiple tube two, with the pass reduction drawing of 10%, obtain the once-combined wire rod that cross section is the circle of diameter 5.2mm; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%; In described Nb/Cu multiple tube, Nb is as inner barrier layer, and Cu is as outer liptinite;
Step 2, as shown in Figure 3, a CuAg alloy bar 2 identical with wire rod 1 once-combined described in step one for 1 size and 6 once-combined wire rods 1 are placed in oxygen-free copper pipe 3 and assemble, obtain secondary multiple tube; A described CuAg alloy bar 2 is positioned at oxygen-free copper pipe 3 center, and once-combined wire rod 1 loads in oxygen-free copper pipe 3 around a CuAg alloy bar 2; In a described CuAg alloy bar 2, the volumn concentration of Ag is 24%, and surplus is Cu; The residual resistance ratio RRR of described oxygen-free copper pipe 3 is not less than 100;
Step 3, pass reduction with 25% to the multiple tube of secondary described in step 2 drawing 3 times, then with 12% pass reduction drawing, obtain the wire rod that cross-sectional diameter is 2mm;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 250MPa
2wire rod; The mutually heat treated temperature of described one-tenth is 650 DEG C, and the time is 2h.
Embodiment 12
The present embodiment is identical with embodiment 11, wherein difference is: the assembling mode of secondary multiple tube as shown in Figure 4, the once-combined wire rod of a CuAg alloy bar 2,61 and 6 the 2nd CuAg alloy bars 4 (cross section is the circle of diameter 1.3mm) identical with described once-combined wire rod 1 for 1 size are placed in oxygen-free copper pipe 3 assemble, obtain secondary multiple tube; In the space of described 2nd CuAg alloy bar 4 between adjacent two once-combined wire rods 1 and oxygen-free copper pipe 3; In described 2nd CuAg alloy bar 4, the volumn concentration of Ag is 24%, and surplus is Cu; The high-strength MgB prepared
2the intensity of wire rod is 260MPa.
The above; it is only preferred embodiment of the present invention; not any restriction is done to the present invention, every above embodiment is done according to invention technical spirit any simple modification, change and equivalent structure change, all still belong in the protection range of technical solution of the present invention.
Claims (8)
1. a high-strength MgB
2the preparation method of wire rod, is characterized in that, the method comprises the following steps:
Step one, by amorphous boron powder, magnesium powder and doping powder according to 1: the atomic ratio of (2-x): x batching, under argon gas atmosphere protection ground and mixed evenly after obtain Precursor Powder, described Precursor Powder is loaded in Nb/Cu multiple tube, with the pass reduction drawing of 10% ~ 15%, obtaining cross section is circular once-combined wire rod, or cross section is orthohexagonal once-combined wire rod; Described doping powder is amorphous carbon or carbide; Described x is 0.05 ~ 0.15; In described Precursor Powder, the mass percentage of oxygen is not more than 0.1%;
Step 2, once-combined wire rod (1) described in 1 CuAg alloy bar (2) and 6 steps one is placed in oxygen-free copper pipe (3) assembles, obtain secondary multiple tube; Or once-combined wire rod (1) described in 1 CuAg alloy bar (2), 6 steps one and 6 the 2nd CuAg alloy bars (4) are placed in oxygen-free copper pipe (3) assemble, obtain secondary multiple tube; A described CuAg alloy bar (2) is positioned at oxygen-free copper pipe (3) center, and once-combined wire rod (1) loads in oxygen-free copper pipe (3) around a CuAg alloy bar (2); Described 2nd CuAg alloy bar (4) is arranged in the space between adjacent two once-combined wire rods (1) and oxygen-free copper pipe (3); Size and the once-combined wire rod (1) of a described CuAg alloy bar (2) are measure-alike;
Step 3, pass reduction with 20% ~ 25%, to the multiple tube of secondary described in step 2 drawing 3 times, are then drawn to required size with the pass reduction of 10% ~ 15%, obtain wire rod;
Step 4, by wire rod described in step 3 argon gas atmosphere protection under carry out into phase heat treatment, obtain the high-strength MgB that intensity is 220MPa ~ 280MPa
2wire rod.
2. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, the quality purity of argon gas described in step one is 99.999%.
3. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, diameter circular described in step one is 3.56mm ~ 8.6mm; Orthohexagonal inscribed circle diameter described in step one is 3.56mm ~ 8.6mm.
4. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, carbide described in step one is titanium carbide.
5. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, in the multiple tube of Nb/Cu described in step one, Nb is as inner barrier layer, and Cu is as outer liptinite.
6. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, the volumn concentration of a CuAg alloy bar (2) described in step 2 and the middle Ag of the 2nd CuAg alloy bar (4) is 18% ~ 24%, and surplus is Cu.
7. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, the residual resistance ratio RRR of oxygen-free copper pipe described in step 2 (3) is not less than 100.
8. the high-strength MgB of one according to claim 1
2the preparation method of wire rod, is characterized in that, become mutually heat treated temperature to be 650 DEG C ~ 800 DEG C described in step 4, the time is 2h.
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