CN100535164C - Fe-36Ni based alloy wire and manufacturing method thereof - Google Patents
Fe-36Ni based alloy wire and manufacturing method thereof Download PDFInfo
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- CN100535164C CN100535164C CNB2006101174434A CN200610117443A CN100535164C CN 100535164 C CN100535164 C CN 100535164C CN B2006101174434 A CNB2006101174434 A CN B2006101174434A CN 200610117443 A CN200610117443 A CN 200610117443A CN 100535164 C CN100535164 C CN 100535164C
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Abstract
The invention relates to an alloy wire material taking Fe-36Ni as the base. The invention is characterized in that the components has the mass percentage that: C occupies 0.15 to 0.40 percent, Si is lower than or equal to 0.59 percent, Mn is lower than or equal to 0.60 percent, P is lower than or equal to 0.025 percent, S is lower than or equal to 0.02 percent, Ni occupies 34.0 to 40.0 percent, Co is lower than or equal to 3.5 percent, Cr is lower than or equal to 0.49 percent, Mo occupies 1.5 to 4.0 percent, NB occupies 0.3 to 1.0 percent, and the residual is Fe and inevitable foreign impurities. The manufacture method of the alloy wire material taking Fe-36Ni as the base in particular comprises the following steps: the alloy component steel ingot of the invention is made into coil rods through forging and hot rolling; the hot rolled coil rods are performed coagulation heat treatment at 1000 to 1150 DEG C; cooling processing is performed within the deformation amount scope of 20 to 75 percent; reduction heat treatment is performed within the scope of 450 to 750 DEG C; the cooling processing with the deformation amount is larger than or equal to 55 percent.
Description
Technical field
The present invention relates to a kind of alloy wire and manufacture method thereof with the low Fe-36Ni of high strength and excellent torsional property and the coefficient of expansion for base.
Background technology
The Fe-36Ni Invar alloy is since invention in 1893, and because of its coefficient of expansion is very low and well-known, they are when 20～100 ℃ and 20～300 ℃, and the coefficient of expansion is respectively≤1.5 * 10
-6/ ℃ and≤5.1 * 10
-6/ ℃, owing to having the extremely low coefficient of expansion (have only common material 1/5～1/10), this alloy has special purposes, for example, can be used for making aluminum stranded conductor steel core in the transmission pressure, can make transmission line have the advantage of underrelaxation degree, the sag of transmission pressure is little when hot operation, and transmitting capacity is significantly improved, and can reduce the height and the density of iron tower.But the intensity of common Invar alloy is very low, is about 400～500MPa, and its use in the low bulk structural part is restricted.
From relevant patent and document, the main method that improves Invar alloy intensity is to serve as that base realizes improving the purpose of alloy strength by adding carbon and carbide forming element with the Fe-36Ni alloy, for example: interpolation C and V make and separate out vanadium carbide in the alloy, rely on this precipitation strength to improve the intensity of alloy, but under the situation of only adding V, the VC precipitate becomes big particle easily, can not reach abundant high strength, common intensity is less than 1100Mpa, and its plasticity, torsional property are relatively poor.
CN 1039438 discloses " Ultra-high-strength Invar alloy and its production methods ", adds tensile strength 〉=1150Mpa that C and Nb make the FeNi Invar alloy, and this invention is not illustrated the torsional property of alloy.
JP2003082439 then discloses and a kind of C, Mo, V has been united interpolation, chemical ingredients is C:0.20～0.40wt%, Si≤0.8wt%, Mn≤1.0wt%, P≤0.050wt%, Mo1.5～6.0wt%, V0.05～1.0wt%, Mo/V 〉=1.0wt%, and (0.3Mo+V) 〉=4C, all the other are iron and unavoidable impurities) formation diffuse type carbide, mean coefficient of linear thermal expansion≤3.7 * 10 of this alloy in the time of 20～230 ℃
-6, 230～290 ℃ of mean coefficient of linear thermal expansion≤10.8 * 10
-6, tensile strength 〉=1300MPa, but the value of reversing of alloy is lower.Therefore, be used to make the high strength of double capacity conductor, the research and development that height reverses Invar alloy are crucial.
Summary of the invention
The object of the present invention is to provide the alloy wire of a kind of Fe-36Ni for base, the intensity of this alloy wire and torsional property compared with prior art improve greatly.
Another object of the present invention is to provide the manufacture method of a kind of Fe-36Ni for the alloy wire of base.
For reaching above-mentioned purpose, the invention provides the alloy wire of a kind of Fe-36Ni for base, its composition weight percent is: C:0.15～0.40; Si≤0.59; Mn≤0.60; P≤0.025; S≤0.02; Ni:34.0～40.0; Co≤3.5; Cr≤0.49; Mo:1.5～4.0; Nb:0.3～1.0; All the other are Fe and inevitable impurity.
Wherein, Mo: Nb 〉=1.5: 1.C＝0.7～1.3(0.063?Mo+0.2?Nb)。
Described Fe-36Ni is the alloy wire of base, also comprises one or both column elements down, and its composition weight percent is: Al :≤0.1; Mg :≤0.0 1; B :≤0.01; Ca :≤0.02; Rare earth metal :≤0.10.
In the Fe-36Ni Invar alloy, add C and Mo, Nb, make it produce solution strengthening and carbide reinforced, obtain high-intensity target thus.Mo and Nb need to add simultaneously, add Mo and Nb simultaneously, then separate out MC, M
2C or M
6The carbide that the C type is trickle, suppress carbide and become oversize particle, because Mo can gather the interface at NbC and matrix consumingly partially, thereby stop the Nb atom in matrix, in the NbC particle, to spread, even like this in the comparatively high temps tempering, also can keep tiny precipitated phase size, thereby bring the increase of alloy strength, the plasticity and the torsional property of alloy wire all reach higher level simultaneously, even do not take value of reversing (100d) of special processing means alloy wire, be easy to reach more than 80 times, and the discreteness of the value of reversing is little.For the carbide that utilizes Mo and Nb is fully realized high strength, regulation is added than for Mo/Nb 〉=1.5, if can not satisfy this ratio, then occurs thick carbide easily.
In order to realize the purpose of alloy high strength and good torsional property, the add-on of C should satisfy C=0.7～1.3 (0.063 Mo+0.2 Nb), just can guarantee under the prerequisite of afore mentioned rules that Mo and Nb carbide separate out fully satisfying, and avoids uncombined carbon to produce.If the add-on of C is greater than the upper limit of above-mentioned condition in the alloy, then can make to have uncombined carbon in the alloy, and when reaching some amount, the plasticity of alloy wire and torsional property will degenerate.In contrast, if, just can well prevent this phenomenon with the fixing uncombined carbon in the alloy of Mo and Nb.If but the add-on of C is less than the lower limit of above-mentioned condition in the alloy, Mo and Nb carbide are separated out insufficient, and the intensity of alloy will not reach requirement of the present invention.
In the present invention, can add a kind of or two kinds of elements in Al, Mg, B, Ca, the rare earth metal in mentioned component, the content of Al and rare earth metal should≤0.1%, Mg, B, Ca≤0.02%.
Below the addition of chemical ingredients and limit reason details are as follows among the present invention just:
C：0.15～0.40wt％
C is the necessary element of carbide precipitate, and the minimum of C 〉=0.15%th is necessary, separates out with the carbide of sufficient amount, thereby significantly improves the work hardening ability of alloy; But the too high meeting of C causes the appearance of uncombined carbon, and the coefficient of expansion of alloy is risen, and C should be limited in below 0.40%.
Si≤0.59wt％
Though Si is effective reductor, Si can increase the coefficient of expansion and unfavorable to torsional property, and is preferably low more good more, and the upper limit is defined as 0.59%.
Mn≤0.60wt％
Mn is the reductor of steel, and also the form that can combine with MnS with S is fixed up S, and is favourable to the raising of hot workability, but unfavorable to the coefficient of expansion and torsional property, should be low more good more, it is defined as≤0.6wt%.
P≤0.025wt％
Because P causes toughness to descend in the segregation of crystal boundary place, it is low more good more to wish, owing to P in Fe, the Ni raw material is lower, is defined as 0.025% on the P.
S≤0.02wt％
S can make hot workability descend, and therefore wishes to reduce it, and its upper limit is defined as 0.020%.
Ni：34.0～40.0wt％
Ni is to guaranteeing that the low bulk performance is essential, and is lower in Ni content 34.0～40.0% scope expansion characters, and for obtaining more low bulk performance, Ni+Co content is controlled at 37.0～39.0% scope the bests.
Nb：0.3～1.0wt％
Nb is as MC, M
8C
7The type carbide is separated out, and intensity and torsional property are improved, and be limited to 0.3% under it, but excessive interpolation then can generate thick carbide, makes torsional property and toughness variation, therefore stipulates to be limited to 1.0% on it.
Cr≤0.49wt％
Cr also is a carbide forming element, can effectively improve intensity, but can increase the coefficient of expansion, thereby the upper limit is defined as 0.49%.
Mo?1.5～4.0wt％
Mo is as fine M
2C or M
6C type carbide forming element can increase the work hardening rate of alloy, and can guarantee that NbC separates out with tiny precipitated phase size, is decided to be 1.5% with its undergage; But the too high coefficient of expansion that causes of the add-on of Mo increases, thereby its upper limit is defined as 4.0%.
Mo/Nb≥1.5
Balance by Mo and Nb adds, and can form the ideal fine carbide and separate out, thereby obtain high intensity and toughness.If satisfy formula, can obtain Mo and Nb composition equilibrated MC or M
8C
7The type carbide, formula numerical value increases, and can form M
2C, these carbide all are effective precipitates to intensity and torsional property, if formula＜1.5 then be difficult to obtain high intensity, wish to be controlled at 〉=2.0.
C＝0.7～1.3(0.063?Mo+0.2?Nb)
In order to obtain sufficient high strength of alloy and stable torsional property and excellent toughness, must satisfy this formula,, C can cause the existence of uncombined carbon if adding excessively, and cross and hang down then fully high strength.
Co≤3.5wt％
Be used for substituting part of nickel, when hope obtains the lower coefficient of expansion, can add appropriate amount, but should the corresponding add-on that reduces Ni.
The content of Al and rare earth metal answers≤0.10%, Mg≤0.01%.、B≤0.01％。、Ca≤0.02％
Al, Ca, Mg, B, rare earth are the elements that adds for deoxidation, help to improve the hot workability of steel, but excessively adding also is disadvantageous.
The preparation method of low bulk high-strength alloy wire rod of the present invention is as follows: alloying constituent steel ingot of the present invention is become wire rod through forging, hot rolling; Gren rod carries out 1000～1150 ℃ solution heat treatment; In 20～75% deflection scopes, carry out cold working; In 450～750 ℃ of scopes, reply thermal treatment; Implement the cold working of 〉=55% deflection.Tensile strength 〉=the 1300MPa of the alloy wire of producing, the coefficient of expansion≤3.0 * 10
-6/ ℃ (20～230 ℃) ,≤10.0 * 10
-6/ ℃ (230～300 ℃).
Wherein, it is fully to dissolve for the carbide that guarantees Mo and Nb that gren rod carries out 1000～1150 ℃ solution heat treatment, carbide is trickle when replying thermal treatment after making alloy wire cold drawn separates out, help alloy work hardening rate, torsional property, flexible raising, solution heat treatment also can be carried out after gren rod is cold drawn, but solution heat treatment is the step that must carry out in the production process.
Here the cold working first that hot rolling is made behind the wire rod has been the prestrain effect, helps separating out trickle and uniform carbide in subgrain boundary in the back answer heat treatment process.In the cold working process, deflection≤20% can not give sufficient prestrain, and if when surpassing 75% deflection, then the recrystallization temperature of alloy descends, and causes after descending a time thermal treatment, is difficult to obtain high intensity.
The answer thermal treatment of carrying out in 450～750 ℃ of temperature ranges is evenly to separate out in parent phase for the carbide that makes Mo and Nb, by this intensity that improves alloy that separates out, the dislocation desity of matrix is descended, and guarantees suitable torsional property.
The cold working of carrying out is subsequently carried out for guaranteeing necessary strength, and this moment, minimum machining deformation amount answered 〉=55%, can obtain the high-strength low-expansion alloy wire of tensile strength greater than 1300MPa thus.
The present invention compared with prior art, have good torsional property and high-intensity while, obtain the lower coefficient of expansion: tensile strength 〉=1300MPa, value of reversing (100d) 〉=80 time, the coefficient of expansion of alloy is lower, and its 20～230 ℃ and 230～290 ℃ of temperature range averages coefficient of linear expansion be respectively≤and 3.0 * 10
-6/ ℃ and≤10.0 * 10
-6/ ℃.Satisfy the application requiring of double capacity conductor.
Embodiment
Below by specific embodiment the present invention is described.
Table 1 is the chemical ingredients and the performance process parameter table of the embodiment of the invention 1～5 and Comparative Examples 1～5.
Table 1
C=A (0.063 Mo+0.2 Nb), coefficient A=0.7～1.3 o'clock material high comprehensive performance.
Cold drawn 1 is meant that the first time of carrying out after the wire rod solution treatment is cold drawn, and cold drawn 2 are meant that the second time of carrying out after wire rod is through cold drawn and timeliness thermal treatment for the first time is cold drawn.
Use the 150Kg vacuum induction melting, casting obtains the 135Kg spindle.Alloy steel ingot is heated to 1180 ℃ of forgings is processed into diameter
Pole.Pole is heated to 1050～1100 ℃ rolls into wire rod, wire rod diameter of phi 12.
Embodiment 1
C：0.24wt％；Si：0.26wt％；Mn：0.60wt％；P：0.01wt％；S：0.02wt％；Ni：38.34wt％；Cr：0.49wt％；Mo：1.52wt％；Nb：1.0wt％；Mo/Nb＝1.52；Ca：0.02wt％。
As table 1, gren rod is carried out 1000 ℃ solution heat treatment, wire rod is carried out cold working, at first, the wire rod in the 75% deflection scope is carried out cold drawn processing, it is cold drawn to carry out the first time, heat-treats then pickling, peeling under 460 ℃ temperature;
Wire rod in the 55% deflection scope is carried out cold drawn processing, it is cold drawn to carry out the second time, under 460 temperature, heat-treat then, on cold drawn finished product, take a sample, tensile strength 1350MPa, the value of reversing (100d) is 153 times, and the coefficient of expansion of alloy is lower, its 20～230 ℃ and 230～290 ℃ of temperature range averages coefficient of linear expansion be respectively≤and 2.19 * 10
-6/ ℃ and≤4.59 * 10
-6/ ℃.Satisfy the application requiring of double capacity conductor.
The concrete steps of embodiment 2～5 are with embodiment 1, this tired no longer one by one stating.
Can find out that from the foregoing description alloy wire of the present invention can obtain good tensile strength, all 〉=1300MPa, torsional property and low bulk excellent performance.In contrast, the value of C, Mo, Nb, Mo/Nb, C=0.7～1.3 (0.063W+0.2V) can not satisfy the comparative example alloy of condition of the present invention, and its tensile strength, torsional property have at least one to be not being met.
Claims (4)
1. a Fe-36Ni is basic alloy wire, it is characterized in that its composition weight percent is:
C：0.15～0.40；
Si≤0.59；
Mn≤0.60；
P≤0.025；
S≤0.02；
Ni：34.0～40.0；
Co≤3.5；
Cr≤0.49；
Mo：1.5～4.0；
Nb：0.3～1.0；
C＝0.7～1.3(0.063Mo+0.2Nb)；
All the other are Fe and inevitable impurity.
2. Fe-36Ni as claimed in claim 1 is the alloy wire of base, it is characterized in that: Mo: Nb 〉=1.5: 1.
3. Fe-36Ni as claimed in claim 1 is the alloy wire of base, it is characterized in that, also comprises one or both column elements down, and its composition weight percent is:
Al：≤0.1；
Mg：≤0.01；
B：≤0.01；
Ca：≤0.02；
Rare earth metal :≤0.10.
4. Fe-36Ni as claimed in claim 1 is the manufacture method of the alloy wire of base, comprises the steps: that specifically described alloying constituent steel ingot becomes wire rod through forging, hot rolling; Gren rod carries out 1000～1150 ℃ solution heat treatment; In 20～75% deflection scopes, carry out cold working; In 450～750 ℃ of scopes, reply thermal treatment; Implement the cold working of 〉=55% deflection.
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| KR101420281B1 (en) * | 2012-10-09 | 2014-08-14 | 고려제강 주식회사 | Wirerope and manufacturing method thereof |
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| CN105543693B (en) * | 2015-12-17 | 2017-07-11 | 东北大学 | A kind of deep cooling milling method of invar steel band |
| CN110546292B (en) * | 2017-04-19 | 2022-04-19 | 山阳特殊制钢株式会社 | High Strength Low Thermal Expansion Alloy Wire |
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| CN108588555B (en) * | 2018-04-17 | 2022-08-09 | 全球能源互联网研究院有限公司 | Alloy steel for overhead conductor, preparation method of alloy steel and overhead conductor |
| CN110541119B (en) * | 2018-05-28 | 2021-07-09 | 宝武特种冶金有限公司 | Low-expansion iron-nickel alloy and manufacturing method thereof |
| CN109852896B (en) * | 2019-04-16 | 2021-04-06 | 常熟理工学院 | Method for manufacturing Fe-36Ni invar alloy plate with low thermal expansion |
| CN114107838A (en) * | 2020-09-01 | 2022-03-01 | 宝武特种冶金有限公司 | High-strength invar alloy wire and manufacturing method thereof |
| CN115094330A (en) * | 2022-07-15 | 2022-09-23 | 东北特殊钢集团股份有限公司 | Precipitation hardening invar alloy and processing method thereof |
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