CN1743490A - High-strength invar alloy and its alloy wire rod production method - Google Patents
High-strength invar alloy and its alloy wire rod production method Download PDFInfo
- Publication number
- CN1743490A CN1743490A CN 200510029930 CN200510029930A CN1743490A CN 1743490 A CN1743490 A CN 1743490A CN 200510029930 CN200510029930 CN 200510029930 CN 200510029930 A CN200510029930 A CN 200510029930A CN 1743490 A CN1743490 A CN 1743490A
- Authority
- CN
- China
- Prior art keywords
- alloy
- wire rod
- invar
- high strength
- cold
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Abstract
A high intensity invariable steel and a production method for it's wire rod characterizes in taking Fe-36Ni alloy as the base added with W, V and C in the following weight percentage: C 0.15 to 0.40, Si is not greater than 0.60, Mn is not greater than 0.8, p is not greater than 0.025, S is not greater than 0.02, Ni: 34.0 to 42.0, co is not greater than 3.5, Cr is not greater than 0.5, Cu is not greater than 0.2, W: 1.5 to 5.0, v 0.3 to 1.2, Mo is not greater than 0.5, the rest is Fe and unavoidable impurities, W.V is greater than 1.5, c=0.9-1.3(0.033w+0.2V). The production method includes: 1, processing the steel ingot into rods then to wire rods (phi=10 to 15mm) 2, applying special twice cold processing deformation and hot process, the twice cold-draw deformations are 20-70%, 55 to 95% then they are hot processed under 450-750 DEG C.
Description
Technical field
The present invention relates to the composition design and the manufacture method thereof of low bulk Invar alloy, refer in particular to the manufacture method of high strength Invar alloy wire rod.
Background technology
Invar alloy belongs to specific alloy, Fe-36Ni Invar alloy (4J36 alloy) is common Invar alloy, since invention in 1893, (coefficient of expansion and alloy material, use temperature are closely related: alloy material is different, coefficient of expansion difference because of its low-down coefficient of expansion; With a kind of alloy material, the use temperature height, average coefficient of expansion α is also higher.The coefficient of expansion of Fe-36Ni Invar alloy is very low, has only 1/5～1/10 of common material.For the 4J36 alloy, GBn 110-87 standard code: in the time of 20～100 ℃, α≤1.5 * 10
-6/ ℃; In general, α recommendation in kind is: in the time of 20～100 ℃, and α=0.8 * 10-6/ ℃, in the time of 20～200 ℃, α=2.0 * 10
-6/ ℃, in the time of 20～300 ℃, α=5.1 * 10
-6/ ℃) and well-known, (be about 400～500MPa), limited its use range, but its intensity is very low so common Fe-36Ni Invar alloy is usually used in the application of non-structural part, as standard scale.
The Invar alloy wire rod is one of principal item of Invar alloy, and the preparation method of conventional Fe-36Ni Invar alloy (4J36 alloy) wire rod is: the standard compliant alloy steel ingot of (1) composition, forge (or rolling mill breaking down) cogging through forging press, and become the alloy pole; (2), become the alloy wire rod, cleanup acid treatment through rolling mill hot-work rolling deformation; (3) behind the alloy wire rod cold deformation first time (once cold drawn), (4J36 alloy room temperature texture is monophasic austenite structure in 900～1050 ℃ of thermal treatments, 900～1050 ℃ of thermal treatments after cold drawn can make cold deformation organize recrystallize, are convenient to the cold deformation second time of alloy); (4) alloy wire rod cold deformation (secondary the is cold drawn) second time becomes cold drawn finished product.
In recent years, the coefficient of expansion is little and Invar alloy that intensity is high (principal feature has two: one, and the coefficient of expansion is little, in the time of 20～100 ℃, α≤1.5 * 10
-6/ ℃, or 20～300 ℃ the time, α≤5.1 * 10
-6/ ℃; The 2nd, the intensity height, greater than 1000MPa) make, because of its structural part purposes (possessing unique physics and mechanical property makes it have special purposes) receives publicity day by day, in power industry, adopt the Invar alloy material that the coefficient of expansion is little, intensity is high to make aluminum stranded conductor steel core in the transmission line, on the one hand, transmission line has the advantage of underrelaxation degree (coefficient of expansion have only common material 1/5～1/10), and little (sag is the sagging height of transmission line to the sag of transmission line when 230 ℃ of hot operations.The coefficient of expansion is little, and sag is little; The intensity height can make the in light weight of material, and the sag of material deadweight is also little), greatly reduce the height and the density of the iron tower that sets up transmission line; On the other hand, can make transmitting capacity significantly improve (coefficient of expansion is less, and the hot operation sag is less, compares the transmitting capacity height with the other materials of same size).
At present, the approach of making the high strength Invar alloy mainly contains three kinds: (1) first kind is based on the Fe-36Ni alloy, by adding Be, utilize Ni3Be intermetallic compound strengthening mechanism to realize the reinforcement of alloy, the advantage of this method is the good (tensile strength 〉=1500MPa) of strengthening effect, shortcoming be the coefficient of expansion of alloy higher (20～100 ℃, α=3.5～4 * 10
-6/ ℃), and the martensitic phase height height of alloy, be unsuitable for using at low temperatures, more seriously the Be unit of Tian Jiaing have severe toxicity, and is unfavorable to environmental protection.(2) second method is to be base with the Fe-36Ni alloy, realize improving the purpose of alloy strength by adding carbon and carbide forming element, usually adopt interpolation C and V to 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, and common intensity is less than 1100Mpa; (3) the third method (PCT patent application of Japanese Daido Steel Co., Ltd, international publication number: WO 03/025239A1) similar substantially to second method, with the Fe-36Ni alloy is base, realize improving the purpose of alloy strength by adding carbon and carbide forming element, add C and Mo simultaneously, the method of V suppresses thickization of carbide, improve intensity and the torsional property (tensile strength 〉=1300MPa that closes effectively, the value of reversing 〉=20), its shortcoming is: add Mo simultaneously, the alloy coefficient of expansion of V is higher, 20～230 ℃ and 230～290 ℃ of temperature ranges, its average coefficient of linear expansion are respectively≤and 3.7 * 10
-6/ ℃ and≤10.8 * 10
-6/ ℃.
Summary of the invention
The present invention develops the production method of a kind of high strength Invar alloy and alloy wire thereof, be characterized in: the composition design that at first is Invar alloy, it is to be base with the Fe-36Ni alloy, adds W, V, the C element of special component, effectively utilizes the strengthening effect to Invar alloy of C, W, V element; Secondly, adopt conventional production process, alloy steel ingot is processed into the alloy pole, be reprocessed into the alloy wire rod; At last, adopt special secondary cold deformation and thermal treatment process, keep the low expansion character and the torsional property of conventional Fe-36Ni Invar alloy, alloy strength is risen to higher level; Finally, make the product performance of Invar alloy wire rod reach the harmony of intensity index, expansion characteristics, torsional property: the coefficient of expansion low (20～240 ℃ the time, α≤2.5 * 10
-6/ ℃; In the time of 20～290 ℃, α≤4.5 * 10
-6/ ℃), torsional property good (value of reversing 〉=40), alloy strength height (〉=1300MPa).Satisfied the application demand of market to the Invar alloy wire rod of high strength, low bulk.
A kind of high strength Invar alloy of the present invention exploitation is characterized in that: be to be base with the Fe-36Ni alloy, and interpolation W, V, C element; The chemical element composition (weight %) of alloy is 0.15～0.40C, Si≤0.60, Mn≤0.8, P≤0.025, S≤0.02,34.0～42.0Ni, Co≤3.5, Cr≤0.5, Cu≤0.2,1.5～5.0W, 0.3～1.2V, Mo≤0.5, all the other are Fe and inevitable impurity; And W/V 〉=1.5, C=0.9～1.3 (0.033W+0.2V).
In the composition of above-mentioned high strength Invar alloy, can add Mo, two kinds of elements of Co 1～2 kind: Mo≤3.0%, Co≤3.5% is to reduce the coefficient of expansion of alloy.
In the composition of above-mentioned high strength Invar alloy, can also add 1～2 kind in Mg, B, Ca, Ce, five kinds of elements of La, the content of addition element≤0.01% is to improve the hot workability of alloy.
In the composition of above-mentioned high strength Invar alloy, when interpolation Mo, two kinds of elements of Co 1～2 kind, can add 1～2 kind in Mg, B, Ca, Ce, five kinds of elements of La simultaneously.
By in alloy, adding C and V, W, make it separate out carbide separately in the present invention, obtain high-intensity target thus, do not add W, only adding separately under the situation of V, can separate out vanadium carbide, but this precipitate becomes oversize particle easily, can not reach abundant high strength.If add W and V simultaneously, then separate out MC, M
2C or M
6The carbide that the C type is trickle suppresses carbide and becomes oversize particle, thereby can improve the intensity of low bulk Invar alloy effectively.For the carbide that utilizes W and V is fully realized high strength, regulation is added than satisfying W/V 〉=1.5, if can not satisfy, then thick carbide can occur.
In order to realize the purpose of alloy high strength and good torsional property, add-on to C must be stipulated, the add-on of carbon should satisfy C=0.9～1.3 (0.033W+0.2V), just can guarantee under the prerequisite of afore mentioned rules that W, V carbide separate out fully satisfying, and avoids uncombined carbon to produce.If there is uncombined carbon in the alloy, and when reaching some amount, distortion just was concentrated in local location when alloy wire reversed, and produced " simple brittle failure " phenomenon thus.In contrast, if, just can well prevent this phenomenon with the fixing uncombined carbon in the alloy of W and V.
Below the addition of chemical ingredients and limit reason details are as follows among the present invention just:
C：0.15～0.40％。C is the necessary element of carbide precipitate, for obtaining enough high strength, and the minimum of C 〉=0.15%th, necessary, but the too high meeting of C causes the appearance of uncombined carbon, C should be limited in below 0.40%.
Si≤0.60％。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 0.60%.
Mn≤0.8％。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≤1.0%.
P≤0.025％。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≤0.020％。S can make hot workability descend, and therefore wishes to reduce it, and its upper limit is defined as 0.020%.
Cu≤0.50％。Cu helps to improve intensity, makes the hot workability variation but add excessive meeting, and thermal expansivity increases, and stipulates to be limited to 0.5% on it.
Ni：34.0～40.0％。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.
W：1.5～5.0％。W separates out as fine MC, M2C or M8C7 type carbide, and the intensity of alloy and torsional property are improved, and for guaranteeing the intensity Schwellenwert, the add-on least restrictive of W is 1.5%.W adds as the too high coefficient of expansion that then can make increases, therefore with 6.0% as the upper limit.
V：0.3～1.2％。V is the same with W to separate out as MC, M8C7 type carbide, 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 1.2% on it.
Cr≤0.5％。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 0.5%.
Mo≤0.5％。Mo is the same as with W fine MC, M
2C or M
8C
7The type carbide forming element, but the add-on of Mo can cause cost to rise and the coefficient of expansion increases, thereby its upper limit is defined as 0.5%.
W/V≥1.5。Balance by W and V adds, and can form the ideal fine carbide and separate out, thereby obtain high intensity and toughness.If satisfy formula, can obtain V and W composition equilibrated MC or M8C7 type carbide, formula numerical value increases, can form M2C, 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＝0.9～1.3(0.033W+0.2V)。In order to obtain 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≤3.5％。Because Co can cause cost to rise, do not add generally speaking, but when wishing to obtain the lower coefficient of expansion, can add, but the add-on of answering corresponding minimizing Ni.
Mg、B、Ca、Ce、La≤0.010％。Ca, Mg, B, rare earth are the hot worked elements that helps to improve steel, therefore wish to add, but excessively adding also are disadvantageous, therefore its upper limit are defined as 0.010%.
The production method of above-mentioned high strength Invar alloy wire rod is characterized in that: (1) adopts conventional production process, and alloy steel ingot is processed into alloy preform, alloy preform is processed into the alloy wire rod again; (2) adopt special secondary cold deformation and thermal treatment process, keep the low expansion character and the torsional property of conventional Fe-36Ni Invar alloy, alloy strength is risen to higher level; Finally, make the product performance of Invar alloy wire rod reach the harmony of intensity index, expansion characteristics, torsional property: the coefficient of expansion low (20～240 ℃ the time, α≤2.5 * 10
-6/ ℃; In the time of 20～290 ℃, α≤4.5 * 10
-6/ ℃), torsional property good (value of reversing 〉=40), alloy strength height (〉=1300MPa).
(1) adopt conventional production process, alloy steel ingot be processed into the alloy preform (alloy preform can be a pole, also can be square billet) of 40～240mm, again alloy preform is processed into the alloy wire rod of φ 10～15mm:
(A) adopt conventional smelting process for production, smelting with the Fe-36Ni alloy is base, adds the above-mentioned high strength Invar alloy of W, V, C element, and is cast into alloy steel ingot;
(B) adopt conventional thermal processing distortion production technique,, forge or rolling mill breaking down cogging, be processed into the alloy preform of 40～240mm through forging press with the standard compliant alloy steel ingot of composition;
(C) adopt conventional thermal processing distortion production technique,, alloy preform is processed into the alloy wire rod of φ 10～15mm through rolling mill hot-work rolling deformation;
(2) adopt special secondary cold deformation and thermal treatment process, keep the low expansion character and the torsional property of conventional Fe-36Ni Invar alloy, alloy strength is risen to higher level:
(A) adopt cold-drawing process, (cold deformation has been the prestrain effect for the first time to the alloy wire rod cold deformation first time, help separating out in the heat treatment process of back trickle and uniform carbide), deflection 20～70% (deflection≤20%, can not give sufficient prestrain, if and when surpassing 70% deflection, then when descending a time thermal treatment, be difficult to obtain high intensity); For the first time behind the cold deformation, alloy cold spare carries out 450～750 ℃ of thermal treatments, and (thermal treatment of carrying out in 450～750 ℃ of temperature ranges is evenly to separate out in parent phase for the carbide that makes W and V, by this intensity that improves alloy that separates out, the dislocation desity of matrix is descended, guarantee suitable torsional property.Thermal treatment temp＜450 ℃, the carbide of alloy is separated out insufficient, can not make alloy wire obtain high strength, and the dislocation desity of matrix descends less, and the cold deformation second time difficulty of alloy is unfavorable for the stable of torsional property; Temperature＞750 ℃ can make the carbide of alloy thick, and matrix can produce part recrystallize phenomenon simultaneously, alloy for the second time in the cold deformation process strengthening effect relatively poor, can not realize intensity index of the present invention=;
(B) adopt cold-drawing process, alloy cold spare is carried out cold deformation (cold deformation carries out for guaranteeing necessary strength for the second time, and minimum amount of finish answers 〉=55%) for the second time, deflection 55～95%; Produce the coefficient of expansion low (20～240 ℃ the time, α≤2.5 * 10
-6/ ℃; In the time of 20～290 ℃, α≤4.5 * 10
-6/ ℃), torsional property good (value of reversing 〉=40), tensile strength height (〉=1300MPa) alloy wire.
Compare with prior art, the present invention has following advantage:
1, design of alloy is reasonable, the intensity height;
2, the alloy wire production technique is simple, and is workable, technology stability is high;
3, the product coefficient of expansion is low, torsional property good, tensile strength is high.
4, production efficiency height, the product percent of pass height.
Specific embodiments
Certain Iron And Steel Company implements patent of the present invention, has produced 5 stoves (1#, 2#, 3#, 4#, 5#) high strength Invar alloy wire rod, and the composition characteristics of high strength Invar alloy is: be to be base with the Fe-36Ni alloy, and interpolation W, V, C element; The chemical element composition (weight %) of alloy is 0.15～0.40C, Si≤0.60, Mn≤0.8, P≤0.025, S≤0.02,34.0～42.0Ni, Co≤3.5, Cr≤0.5, Cu≤0.2,1.5～5.0W, 0.3～1.2V, Mo≤0.5, all the other are Fe and inevitable impurity; And W/V 〉=1.5, C=0.9～1.3 (0.033W+0.2V).In addition, examination has been refined 5 stoves (6#, 7#, 8#, 9#, 10#) composition not in full conformity with relatively alloy 5 stoves (6#, 7#, 8#, 9#, 10#) of the present invention.
The production method of above-mentioned high strength Invar alloy wire rod, it is characterized in that (1) employing conventional production process, alloy steel ingot is processed into the alloy pole, be reprocessed into the alloy wire rod: (A) adopt conventional smelting process for production, smelting with the Fe-36Ni alloy is base, add the above-mentioned high strength Invar alloy of W, V, C element, and be cast into alloy steel ingot; As use the 150Kg vacuum induction melting, and casting obtains the 135Kg spindle, and alloy composition is shown in Table 1.(B) adopt conventional thermal processing distortion production technique (1180 ℃ of alloy steel ingot Heating temperatures),, forge or rolling mill breaking down cogging, be processed into the alloy preform of φ 50mm through forging press with the standard compliant alloy steel ingot of composition; (C) adopt conventional thermal processing distortion production technique (1050～1100 ℃ of Heating temperatures),, alloy preform is processed into φ 12mm (the alloy wire rod of φ 10～15mm) through rolling mill hot-work rolling deformation; (2) adopt special secondary cold deformation and thermal treatment process, the low expansion character and the torsional property that keep conventional Fe-36Ni Invar alloy, alloy strength is risen to higher level: (A) adopt cold-drawing process, to the alloy wire rod cold deformation first time, deflection 35～50% (20～70%); Behind the cold deformation, alloy cold spare carries out 450～700 ℃ of thermal treatments for the first time; (B) adopt cold-drawing process, alloy cold spare is carried out the cold deformation second time, deflection 55～85% (55～95%); Behind the cold deformation, then carry out pickling, peeling for the second time; Produce the coefficient of expansion low (20～240 ℃ the time, α≤2.5 * 10
-6/ ℃; In the time of 20～290 ℃, α≤4.5 * 10
-6/ ℃), torsional property good (value of reversing 〉=40), tensile strength height (〉=1300MPa) alloy wire (cold deformation parameter and test result see Table 2).
Can find out from the result of table 1, table 2: implement 5 stoves (1#, 2#, 3#, 4#, 5#) the high strength Invar alloy wire rod that the present invention produces, can obtain good tensile strength (〉=1300MPa), torsional property and low bulk excellent performance, qualification rate 100%.In contrast, the value of C, W, V, W/V, C=0.9～1.3 (0.033W+0.2V) can not satisfy relatively alloy of 5 stoves of condition of the present invention (6#, 7#, 8#, 9#, 10#), and its tensile strength, torsional property have at least one to be not being met.
Show thus, it is epochmaking in the present invention the chemical ingredients of alloy being defined in the application range, but the production method of alloy wire also is important, making creates conditions meets patent claim, both combinations, just can when guaranteeing that alloy has good torsional property and utmost point low thermal coefficient of expansion, obtain gratifying high strength effect.Satisfy customer requirements and market demand, remarkable in economical benefits.
High strength Invar alloy chemical ingredients, % table 1
| C | Si | Mn | P | S | Ni | Cr | W | V | Mo | W/V | A | Other | ||
| The invention alloy | 1# | 0.21 | 0.27 | 0.30 | ＜0.01 | 0.004 | 38.48 | 0.01 | 2.16 | 0.63 | 0.10 | 3.43 | 1.06 | / |
| 2# | 0.25 | 0.26 | 0.29 | ＜0.01 | 0.004 | 38.20 | 0.01 | 2.50 | 0.67 | 0.01 | 3.73 | 1.15 | 0.0015Mg | |
| 3# | 0.28 | 0.28 | 0.31 | ＜0.01 | 0.005 | 37.98 | 0.01 | 3.12 | 0.70 | 0.01 | 4.46 | 1.15 | 0.0016Ca | |
| 4# | 0.22 | 0.27 | 0.30 | ＜0.01 | 0.004 | 38.15 | 0.02 | 2.80 | 0.56 | 0.01 | 5.0 | 1.08 | / | |
| 5# | 0.23 | 0.30 | 0.40 | ＜0.01 | 0.004 | 38.10 | 0.02 | 3.20 | 0.36 | 0.01 | 8.9 | 1.21 | / | |
| Compare alloy | 6# | 0.23 | 0.31 | 0.29 | ＜0.01 | 0.004 | 37.91 | 0.02 | 0.44 | 1.08 | 0.02 | 0.45 | 1.00 | / |
| 7# | 0.24 | 0.30 | 0.29 | ＜0.01 | 0.004 | 38.67 | 0.02 | 0.41 | 1.10 | 0.02 | 0.37 | 1.03 | / | |
| 8# | 0.14 | 0.30 | 0.28 | ＜0.01 | 0.004 | 38.15 | 0.02 | 2.30 | 0.75 | 0.02 | 3.06 | 0.63 | / | |
| 9# | 0.35 | 0.29 | 0.31 | ＜0.01 | 0.004 | 37.89 | 0.02 | 2.00 | 0.51 | 0.02 | 3.92 | 2.08 | / | |
| 10 # | 0.25 | 0.29 | 0.32 | ＜0.01 | 0.005 | 38.12 | 0.02 | 0.08 | 0.62 | 2.93 |
Annotate: carbon content C=A (0.033W+0.2V), the present invention can be satisfied in A=0.9～1.3.
Cold deformation parameter and table with test results 2
| Once cold drawn % | Thermal treatment ℃ | The cold drawn % of secondary | Rm Mpa | Reverse L=100d | The coefficient of expansion * 10 -6 | |||
| 20～240℃ | 20～300℃ | |||||||
| The invention alloy | 1# | 50 | 650 | 80 | 1300 | 101 | 1.61 | 3.12 |
| 2# | 40 | 650 | 85 | 1400 | 61 | 1.85 | 3.25 | |
| 3# | 45 | 670 | 70 | 1430 | 45 | 1.97 | 3.47 | |
| 4# | 35 | 650 | 90 | 1320 | 49 | 1.76 | 3.31 | |
| 5# | 60 | 660 | 65 | 1300 | 78 | 1.83 | 3.66 | |
| Compare alloy | 6# | 40 | 650 | 80 | 1220 | 71 | 2.67 | 3.45 |
| 7# | 40 | 650 | 80 | 1190 | 82 | 2.85 | 3.47 | |
| 8# | 40 | 650 | 80 | 1200 | 98 | 2.21 | 3.55 | |
| 9# | 40 | 650 | 80 | Brittle failure | 4 | 2.15 | 3.86 | |
| 10# | 40 | 650 | 80 | 1310 | 75 | 3.55 | 4.72 | |
Claims (5)
1, a kind of high strength Invar alloy is characterized in that with the Fe-36Ni alloy be base, adds W, V, C element; The chemical element composition (weight %) of alloy is: 0.15～0.40C, Si≤0.60, Mn≤0.8, P≤0.025, S≤0.02,34.0～42.0Ni, Co≤3.5, Cr≤0.5, Cu≤0.2,1.5～5.0W, 0.3～1.2V, Mo≤0.5, all the other are Fe and inevitable impurity; And W/V 〉=1.5, C=0.9～1.3 (0.033W+0.2V).
2, a kind of high strength invar according to claim 1 closes, and it is characterized in that in the composition of steel, can add Mo, two kinds of elements of Co 1～2 kind: Mo≤3.0%, Co≤3.5%.
3, a kind of high strength invar according to claim 1 closes, and it is characterized in that in the composition of steel, can also add 1～2 kind in Mg, B, Ca, Ce, five kinds of elements of La, the content of addition element≤0.01%.
4, a kind of high strength invar according to claim 1 closes, and it is characterized in that in the composition of steel, when interpolation Mo, two kinds of elements of Co 1～2 kind, can add 1～2 kind in Mg, B, Ca, Ce, five kinds of elements of La simultaneously.
5, the production method of above-mentioned high strength Invar alloy wire rod is characterized in that: (1) adopts conventional production process, and alloy steel ingot is processed into alloy preform, is reprocessed into the alloy wire rod; (2) adopt special secondary cold deformation and thermal treatment process; Finally, make the product performance of Invar alloy wire rod reach the coefficient of expansion low (20～240 ℃ the time, α≤2.5 * 10
-6/ ℃; In the time of 20～290 ℃, α≤4.5 * 10
-6/ ℃), torsional property good (value of reversing 〉=40), alloy strength height (〉=1300MPa):
(1) adopt conventional production process, alloy steel ingot is processed into the alloy preform of 40～240mm, alloy preform can be a pole, also can be square billet, alloy preform is processed into the alloy wire rod of φ 10～15mm again:
(A) adopt conventional smelting process for production, smelting with the Fe-36Ni alloy is base, adds the above-mentioned high strength Invar alloy of W, V, C element, and is cast into alloy steel ingot;
(B) adopt conventional thermal processing distortion production technique,, forge or rolling mill breaking down cogging, be processed into the alloy preform of 40～240mm through forging press with the standard compliant alloy steel ingot of composition;
(C) adopt conventional thermal processing distortion production technique,, alloy preform is processed into the alloy wire rod of φ 10～15mm through rolling mill hot-work rolling deformation;
(2) adopt special secondary cold deformation and thermal treatment process, keep the low expansion character and the torsional property of conventional Fe-36Ni Invar alloy, alloy strength is risen to higher level:
(A) adopt cold-drawing process, the alloy wire rod is carried out the cold deformation first time, deflection 20～70%; Behind the cold deformation, alloy cold spare carries out 450～750 ℃ of thermal treatments for the first time;
(B) adopt cold-drawing process, alloy cold spare is carried out the cold deformation second time, deflection 55～95%; Produce alloy wire.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2005100299300A CN100447275C (en) | 2005-09-23 | 2005-09-23 | High-strength invar alloy and its alloy wire rod production method |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CNB2005100299300A CN100447275C (en) | 2005-09-23 | 2005-09-23 | High-strength invar alloy and its alloy wire rod production method |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN1743490A true CN1743490A (en) | 2006-03-08 |
| CN100447275C CN100447275C (en) | 2008-12-31 |
Family
ID=36139011
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2005100299300A Active CN100447275C (en) | 2005-09-23 | 2005-09-23 | High-strength invar alloy and its alloy wire rod production method |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN100447275C (en) |
Cited By (20)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102041445A (en) * | 2011-01-21 | 2011-05-04 | 哈尔滨工业大学 | Preparation method of high-strength ultralow-expansion invar-based composite material |
| CN101376951B (en) * | 2007-08-28 | 2011-09-21 | 宝山钢铁股份有限公司 | High strength wire rod for bridge stay cable and suspended cable galvanized steel wire, and manufacturing method thereof |
| CN102888557A (en) * | 2011-07-18 | 2013-01-23 | 宝山钢铁股份有限公司 | High-strength and low-expansion coefficient alloy wire and manufacturing method thereof |
| CN101678493B (en) * | 2007-05-09 | 2014-05-28 | 科诺科菲利浦公司 | Seam-welded 36 Ni-Fe alloy structures and methods of making and using same |
| CN105127234A (en) * | 2015-09-09 | 2015-12-09 | 河北星耀稀有金属材料有限公司 | Processing method of niobium-zirconium alloy wire |
| CN105316575A (en) * | 2014-06-11 | 2016-02-10 | 丹阳市凯鑫合金材料有限公司 | Cold-heading wire for resonance rod and production method thereof |
| CN105316576A (en) * | 2014-07-31 | 2016-02-10 | 宝钢特钢有限公司 | FeNi invar alloy with good welding property |
| CN105506474A (en) * | 2016-01-11 | 2016-04-20 | 河北钢铁股份有限公司 | Carbide-enhanced type invar alloy wire and preparing method thereof |
| RU2581313C1 (en) * | 2014-12-08 | 2016-04-20 | Публичное акционерное общество специального машиностроения и металлургии "Мотовилихинские заводы" | Method of processing carbon-containing invar alloy |
| CN106269967A (en) * | 2015-06-06 | 2017-01-04 | 丹阳市凯鑫合金材料有限公司 | A kind of method making invar bar |
| CN106311791A (en) * | 2015-06-16 | 2017-01-11 | 丹阳市凯鑫合金材料有限公司 | Economic and environmentally friendly method for producing invar steel wire rod coils |
| CN108588555A (en) * | 2018-04-17 | 2018-09-28 | 全球能源互联网研究院有限公司 | A kind of aerial condutor steel alloy, steel alloy preparation method and aerial condutor |
| CN108962430A (en) * | 2018-07-19 | 2018-12-07 | 河北环亚线缆有限公司 | A kind of heat-resisting times of capacity clearance type aluminium alloy nickel coat cobalt alloy core aluminium alloy aerial twisted wire |
| JPWO2018193810A1 (en) * | 2017-04-19 | 2019-04-25 | 山陽特殊製鋼株式会社 | High strength low thermal expansion alloy wire |
| JPWO2018193809A1 (en) * | 2017-04-19 | 2019-04-25 | 山陽特殊製鋼株式会社 | High strength low thermal expansion alloy |
| CN109746455A (en) * | 2019-03-19 | 2019-05-14 | 湖南恒基粉末科技有限责任公司 | A kind of cupric kovar alloy and preparation method thereof |
| CN110541119A (en) * | 2018-05-28 | 2019-12-06 | 宝钢特钢有限公司 | Low-expansion iron-nickel alloy and manufacturing method thereof |
| CN111687236A (en) * | 2019-11-19 | 2020-09-22 | 江苏中天科技股份有限公司 | Preparation method of coated alloy wire |
| CN113195763A (en) * | 2019-03-26 | 2021-07-30 | 日本铸造株式会社 | Low thermal expansion alloy having excellent low temperature stability and method for producing same |
| CN114107829A (en) * | 2020-09-01 | 2022-03-01 | 宝武特种冶金有限公司 | High-strength low-expansion invar alloy wire |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS61183443A (en) * | 1985-02-07 | 1986-08-16 | Daido Steel Co Ltd | Low thermal expansion material |
| JPH06145905A (en) * | 1992-11-16 | 1994-05-27 | Daido Steel Co Ltd | Fe-ni alloy excellent in corrosion resistance |
| CN1151306C (en) * | 2002-09-13 | 2004-05-26 | 钢铁研究总院 | High-strength low-expanded alloy structure steel material |
-
2005
- 2005-09-23 CN CNB2005100299300A patent/CN100447275C/en active Active
Cited By (26)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101678493B (en) * | 2007-05-09 | 2014-05-28 | 科诺科菲利浦公司 | Seam-welded 36 Ni-Fe alloy structures and methods of making and using same |
| CN101376951B (en) * | 2007-08-28 | 2011-09-21 | 宝山钢铁股份有限公司 | High strength wire rod for bridge stay cable and suspended cable galvanized steel wire, and manufacturing method thereof |
| CN102041445A (en) * | 2011-01-21 | 2011-05-04 | 哈尔滨工业大学 | Preparation method of high-strength ultralow-expansion invar-based composite material |
| CN102888557B (en) * | 2011-07-18 | 2014-10-29 | 宝钢特钢有限公司 | High-strength and low-expansion coefficient alloy wire and manufacturing method thereof |
| CN102888557A (en) * | 2011-07-18 | 2013-01-23 | 宝山钢铁股份有限公司 | High-strength and low-expansion coefficient alloy wire and manufacturing method thereof |
| CN105316575A (en) * | 2014-06-11 | 2016-02-10 | 丹阳市凯鑫合金材料有限公司 | Cold-heading wire for resonance rod and production method thereof |
| CN105316576A (en) * | 2014-07-31 | 2016-02-10 | 宝钢特钢有限公司 | FeNi invar alloy with good welding property |
| RU2581313C1 (en) * | 2014-12-08 | 2016-04-20 | Публичное акционерное общество специального машиностроения и металлургии "Мотовилихинские заводы" | Method of processing carbon-containing invar alloy |
| CN106269967A (en) * | 2015-06-06 | 2017-01-04 | 丹阳市凯鑫合金材料有限公司 | A kind of method making invar bar |
| CN106311791A (en) * | 2015-06-16 | 2017-01-11 | 丹阳市凯鑫合金材料有限公司 | Economic and environmentally friendly method for producing invar steel wire rod coils |
| CN105127234A (en) * | 2015-09-09 | 2015-12-09 | 河北星耀稀有金属材料有限公司 | Processing method of niobium-zirconium alloy wire |
| CN105506474A (en) * | 2016-01-11 | 2016-04-20 | 河北钢铁股份有限公司 | Carbide-enhanced type invar alloy wire and preparing method thereof |
| CN110546292A (en) * | 2017-04-19 | 2019-12-06 | 山阳特殊制钢株式会社 | high-strength low-thermal expansion alloy wire |
| 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 |
| JPWO2018193810A1 (en) * | 2017-04-19 | 2019-04-25 | 山陽特殊製鋼株式会社 | High strength low thermal expansion alloy wire |
| JPWO2018193809A1 (en) * | 2017-04-19 | 2019-04-25 | 山陽特殊製鋼株式会社 | High strength low thermal expansion alloy |
| CN108588555A (en) * | 2018-04-17 | 2018-09-28 | 全球能源互联网研究院有限公司 | A kind of aerial condutor steel alloy, steel alloy preparation method and aerial condutor |
| CN110541119A (en) * | 2018-05-28 | 2019-12-06 | 宝钢特钢有限公司 | Low-expansion iron-nickel alloy and manufacturing method thereof |
| 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 |
| CN108962430A (en) * | 2018-07-19 | 2018-12-07 | 河北环亚线缆有限公司 | A kind of heat-resisting times of capacity clearance type aluminium alloy nickel coat cobalt alloy core aluminium alloy aerial twisted wire |
| CN109746455A (en) * | 2019-03-19 | 2019-05-14 | 湖南恒基粉末科技有限责任公司 | A kind of cupric kovar alloy and preparation method thereof |
| CN113195763A (en) * | 2019-03-26 | 2021-07-30 | 日本铸造株式会社 | Low thermal expansion alloy having excellent low temperature stability and method for producing same |
| CN113195763B (en) * | 2019-03-26 | 2022-02-18 | 日本铸造株式会社 | Low thermal expansion alloy having excellent low temperature stability and method for producing same |
| CN111687236A (en) * | 2019-11-19 | 2020-09-22 | 江苏中天科技股份有限公司 | Preparation method of coated alloy wire |
| CN111687236B (en) * | 2019-11-19 | 2021-07-23 | 江苏中天科技股份有限公司 | Preparation method of coated alloy wire |
| CN114107829A (en) * | 2020-09-01 | 2022-03-01 | 宝武特种冶金有限公司 | High-strength low-expansion invar alloy wire |
Also Published As
| Publication number | Publication date |
|---|---|
| CN100447275C (en) | 2008-12-31 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN1743490A (en) | High-strength invar alloy and its alloy wire rod production method | |
| CN100535164C (en) | Fe-36Ni based alloy wire and manufacturing method thereof | |
| CN100507055C (en) | Yield strength 700MPa grade atmospheric corrosion resistant steel and method for manufacturing same | |
| CN1117170C (en) | Cold workable steel bar or wire and process | |
| CN109628836B (en) | High-strength anti-seismic fire-resistant steel for building structure and preparation method thereof | |
| KR20200019459A (en) | Twinning/transformation induced plasticity high entropy steels and method for manufacturing the same | |
| CN103060678A (en) | Medium temperature deformation nanometer austenite enhanced plasticized steel and preparation method thereof | |
| JPH1036938A (en) | Steel for producing metal mold for injection molding of plastic | |
| KR101910938B1 (en) | Cr Filament Reinforced CrMnFeNiCu High Entropy Alloy And Method for Manufacturing The Same | |
| CN114086040A (en) | Aluminum-magnesium-silicon-scandium-zirconium alloy and preparation method thereof | |
| CN109295346B (en) | High-conductivity soft aluminum alloy and preparation method and application thereof | |
| KR100910332B1 (en) | Invar alloy wire excellent in strength and turning characteristics and method for production thereof | |
| CN1240497C (en) | High-carbon and chronmium bearing steel wire for direct drawing and its making process | |
| CN113737065B (en) | Aluminum alloy, preparation method and application | |
| CN112760568B (en) | High-strength high-plasticity low-density steel and preparation method thereof | |
| CN101709444B (en) | Thermal treatment method for lead-free aluminum alloy | |
| CN1131702A (en) | Iron-nickel alloy having low coefficient of expansion | |
| CN102162071B (en) | Limit mandrel steel material for rolled tubes and preparation method thereof | |
| CN111172439A (en) | Refined grain magnesium alloy and preparation method thereof | |
| CN116287931A (en) | Method for remarkably improving strength and hardness of entropy alloy in VCoNi | |
| CN102605249A (en) | Manganese and boron series low-carbon microalloy high-strength non-quenched and tempered steel and production method thereof | |
| KR101193655B1 (en) | Silicon-added high manganese steel having high strength and large ductility and method for manufacturing the same | |
| CN110997962B (en) | Hot rolled steel sheet having excellent strength and elongation and method for manufacturing the same | |
| CN112267050A (en) | High-strength and high-toughness 5-series aluminum alloy and preparation method thereof | |
| CN102605211A (en) | Low density, high strength and high plasticity titanium alloy |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant |