CN104451339B - Low nickel ageing strengthening sections abros and preparation method - Google Patents
Low nickel ageing strengthening sections abros and preparation method Download PDFInfo
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- CN104451339B CN104451339B CN201410809009.7A CN201410809009A CN104451339B CN 104451339 B CN104451339 B CN 104451339B CN 201410809009 A CN201410809009 A CN 201410809009A CN 104451339 B CN104451339 B CN 104451339B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C30/00—Alloys containing less than 50% by weight of each constituent
- C22C30/02—Alloys containing less than 50% by weight of each constituent containing copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C19/00—Alloys based on nickel or cobalt
- C22C19/03—Alloys based on nickel or cobalt based on nickel
- C22C19/05—Alloys based on nickel or cobalt based on nickel with chromium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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Abstract
The present invention relates to a kind of low nickel ageing strengthening sections abros, the weight percentage of the alloy each component is：Ni：36.0~42.0%；Cr：19.0~25.0%；Mo：3.0~6.0%；Cu：1.0~3.50%；Ti：1.5~3.0%；Al：0.2~0.6%；Nb≤0.5%；C≤0.03%, Si≤0.5%, Mn≤0.5%；S≤0.0010；P≤0.005；Trace element 0.01~0.6%；Fe is surplus.The alloy has the high-strength of existing iron nickel base alloy, high-ductility, high-corrosion resistance, and in contrast, it is also lower with more preferable hot-working character, cost.
Description
Technical field
The present invention relates to a kind of metal material, more particularly to a kind of low nickel ageing strengthening sections abros and preparation
Method.
Background technology
Ni-based structural material generally also has in addition to matrix element nickel containing chromium, molybdenum, niobium, tungsten, copper, iron, titanium and aluminium etc.
Beneficial element, it can be used as high temperature alloy or corrosion resistant alloy.Because the nickel content of nickel-base alloy is very high, mass fraction is more than 50%,
Even as high as 80%, therefore material cost is higher, there is certain negative effect for large-scale promotion application.On the other hand, by
Nickel content is too high in alloy, and thermoplasticity is poor, and high temperature hot deformation resistance is larger, is adapted to the warm area of deformation narrower, therefore difficult processing
Degree is very big, process costs are very high, is also a unfavorable factor for commercial introduction.Compared with nickel-base alloy, the Ni-based conjunction of iron
Gold substitutes more nickel with part iron, while still contains the beneficial elements such as higher or appropriate chromium, molybdenum, copper, titanium and aluminium,
On the basis of not changing stable austenite basal body structure, can by composition and the process matching intensity different with control acquisitions, firmly
Degree and toughness plasticity.And due to the downward of nickel content, or even can turn down to 30% (Fe+Ni >=50%), therefore there is obvious valency
Lattice advantage, there is the gesture that can substitute Langaloy greatly in some application scenarios, receive the extensive concern of academia and industrial quarters.
Although the nickel content of iron nickel base alloy is much lower compared with nickel-base alloy, actually alloy content still compares
Height, causes that thermoplasticity is not good enough, high temperature hot deformation resistance is big, deformation warm area is narrow, compared with low alloy material, the heat of iron nickel base alloy
Difficulty of processing is still larger, and process costs are still higher.Therefore similar with Langaloy is that iron nickel base alloy is generally still difficult to
Tubing is manufactured by the technique of hot-puncturing process, tubulation, only minority can only can pass through heat by way of mechanical punching mostly
The technique tubulation of extruding.
On the other hand, for ageing strengthening type alloy, the performance level and microstructure of alloy are closely related, such as brilliant
Grain size, the form of carbide and distribution, the size of intermetallic compound phase and distribution etc., these factors are by Technology for Heating Processing
Come what is controlled.The heat treatment of general ageing strengthening sections nickel-base alloy is made up of solution treatment, intermediate treatment and Ageing Treatment.Greatly
Alloy part is required to the two essential steps of Ageing Treatment after being first dissolved.Have some researchs at present to attempt to use
Direct aging heat treatment substitutes the Technology for Heating Processing for needing two or more step, to shorten technological process, improve production efficiency, drop
Low energy expenditure, but not yet obtain and significantly break through.
The content of the invention
It is an object of the invention to provide a kind of low nickel ageing strengthening sections abros and preparation method, alloy tool
There are the high-strength of existing Fe-Ni, high-ductility, a high-corrosion resistance, and compared with existing iron-Ni-based, have more preferable
Hot-working character, cost is lower.
The technical scheme is that：
Low nickel ageing strengthening sections abros, the weight percentage of the alloy each component are：Ni：36.0~
42.0%；Cr：19.0~25.0%；Mo：3.0~6.0%；Cu：1.0~3.50%；Ti：1.5~3.0%；Al：0.2~
0.6%；Nb≤0.5%；C≤0.03%, Si≤0.5%, Mn≤0.5%；S≤0.0010；P≤0.005；Trace element 0.01
~0.6%；Fe is surplus.
The preferable technical scheme of alloy of the present invention is that the weight percentage of alloy each component is：Ni：38.0~
42.0%；Cr：20.0~23.0%；Mo：3.0~6.0%；Cu：1.0~3.50%；Ti：1.5~3.0%；Al：0.3~
0.6%；Nb≤0.5%；C≤0.03%, Si≤0.5%, Mn≤0.5%；S≤0.0010；P≤0.005；Trace element 0.01
~0.6%；Fe is surplus.
The trace element is V, Zr, B.
V in the trace element：0.01~0.5%, Zr：0.01~0.1%, B：0.001~0.01%.
The preparation method of low nickel ageing strengthening sections abros, each alloy compositions, vacuum are taken according to said ratio
Induction melting, is cast into pole, and electroslag remelting is into steel ingot, Homogenization Treatments, hot forging or hot rolling or hot extrusion, cold rolling or cold-drawn system
Cheng Guan, rod or sheet material, then be heat-treated：2~20 hours are incubated in 700~760 DEG C of air, with 40~60 DEG C per hour
Speed be furnace-cooled to 620~680 DEG C, then be incubated 2~20 hours.
The Homogenization Treatments temperature is 1160~1190 DEG C, the time is 24~72 hours.
Warm and hot forging temperature is 950~1150 DEG C, soaking time is 60~120 minutes；Hot-rolled temperature be 1000~1200 DEG C,
Soaking time is 60~120 minutes；1000~1200 DEG C of extrusion temperature.
The summation of described two soaking time sections is no less than 10 hours.
The time of the heat treatment is no more than 20 hours.
The main function for inventing each element in the alloy is as follows：
(1)Ni：The Ni of high level is to obtain excellent anticorrosive performance, particularly anticorrosion stress-resistant and the corruption of sulfide stress
Lose the important foundation of cracking ability.More Ni is substituted with part Fe, while material cost is reduced, can obtain with it is Ni-based
The stable austenitic matrix of alloy identical.
(2)Cr：Relatively high Cr contents are to obtain the guarantee of corrosion resistance, particularly improve alloy in Oxidant
The key of anti-corrosion capability.But too high Cr contents will promote the precipitation of σ phases, and then damage the heat endurance and thermoplasticity of alloy.
(3)Mo：Higher Mo contents are primarily to improve the local corrosion abilities such as the resistance to spot corrosion of alloy, corrosion at a seam, especially
Improve corrosive power of the alloy in halide ion, reductant.But too high Mo contents can equally promote the precipitation of σ phases,
It is harmful to the heat endurance and thermoplasticity of alloy.
(4)Cu：Appropriate Cu contents are advantageous to improve corrosion resistance of the alloy in reductant.In addition there is research
Show that Cu can separate out rich Cu phases in some alloys after medium temperature long-time timeliness, so as to be beneficial to enduring quality, but anti-corrosion
In alloy, there is not been reported for the performance of Cu this respects.
(5)Nb：Appropriate high Nb can form ageing strengthening phase γ "-Ni3Nb, but too high Nb contents can in as cast condition mistake
Divide segregation, considerably increase the difficulty of follow-up Homogenization Treatments.Iron in Ni contents " deficiency " is Ni-based or low nickel alloy in, Nb is more
It is to be added as carbide former mostly, reduces the formation of chromium carbide, ensures the corrosion resistance of alloy.
(6)Ti、Al：A small amount of Ti, Al has a deoxidation, and the ageing strengthening effect of appropriate Ti, Al addition to alloy has
Positive role, promote ageing strengthening phase γ '-Ni3Effective precipitation of (Al, Ti), alloy is contributed to obtain high intensity and high tenacity.
On the other hand, because Ti, Al are easy scaling loss elements, too high Ti, Al can increase melting and remelting stage Composition Control and heat
The difficulty of processing.
(7)Si、Mn：A small amount of Si, Mn have deoxidation, but in high alloy, Si, Mn are to being harmful to the precipitation of interphase very
Sensitivity, complicate precipitated phase and damage the heat endurance beneficial to precipitated phase, add control difficulty, it usually needs strict control
System.
(8)C：Have solution strengthening effect, also can stable austenite matrix, but too high C content can not only damage alloy
Decay resistance, and welding performance is also harmful to.
(9)V、Zr、B；Healthy trace elements with household V, Zr, B and its accurate proportioning are of great benefit to the hot-working character of alloy.
Alloy of the present invention in the higher chromium of the middle addition of iron-Ni-based, molybdenum content, obtain while optimize Ni, Fe, Cr, Mo,
The main contents such as Ti, Al, more Ni is especially substituted with more Fe, while add the technique element such as micro V, Zr, B, with
Improve the hot-workability of alloy, reduce the tendency of hot tearing in hot procedure.Alloy of the present invention is ageing strengthening sections
Ni-based austenitic alloy, γ ' Strengthening and Toughening phases can be separated out by appropriate heat treatment, so as to obtain higher intensity, hardness and
Toughness plasticity, simultaneously because nickel, chromium, molybdenum content are high, decay resistance is strong, and particularly stress corrosion dehiscence resistant is very capable.
Alloy of the present invention with solution strengthening type is Ni-based or iron nickel base alloy compared with, intensity is higher and can pass through timeliness
Heat treatment manufacture is relatively large or compared with complex parts；Compared with the iron nickel base alloy of other ageing strengthening types, due to micro beneficial to member
The supplying of element, thermoplasticity are improved, and hot cracking tendency reduces in hot procedure, are more easy to make heavy wall using the method for hot extrusion
Tubing, overall craft performance is more excellent, additionally due to taking more low nickel-content to design, design of material cost has declined；With timeliness
Enhanced type Langaloy is compared, and part of nickel is instead of with more iron, but still has stable austenitic matrix structure, simultaneously
Equal obdurability rank is may also reach up, more significant advantage is to significantly reduce material cost, and cost performance is very prominent.
Alloy of the present invention can still obtain together compared with typical ageing strengthening sections nickel-base alloy, using low nickel-content
Deng high intensity, high toughness plasticity, and outstanding decay resistance, therefore material cost is lower；On the other hand, have due to micro
The addition of beneficial element, thermoplasticity are obviously improved, and hot-working difficulty reduces, and lumber recovery improves, or even can use hot-extrusion method system
Standby seamless tubular goods, processing performance have more advantage；Additionally due to the use of unique direct aging heat treatment, Technology for Heating Processing flow become
Short, energy resource consumption reduces, and cost benefit significantly improves.
Alloy of the present invention, it can be used for the such as high sulfur-containing oil-gas exploitation of various highly corrosive environments, petrochemical industry, change
The field such as engineering and ocean engineering, is such as used for the high sulfur-containing oil-gas Mining Equipment material of HTHP, sulfur-containing oil-gas downhole tool,
Key member, and completion drill collar etc..
Brief description of the drawings
Fig. 1 is that alloy of the present invention carries out aging heat treatment room-temperature mechanical property again after different temperatures is dissolved；
Fig. 2 is that alloy of the present invention is carrying out different temperatures aging heat treatment room-temperature mechanical property after solid solution；
Fig. 3 is that room-temperature mechanical property of the alloy of the present invention through solid solution+timeliness and direct aging heat treatment contrasts；
Fig. 4 is metallographic structure of the alloy of the present invention through solid solution+aging state；
Fig. 5 is the metallographic structure of direct aging state after alloy extrusion of the present invention.
Embodiment
One, embodiments
The weight percentage such as institute of table 1 of low nickel ageing strengthening sections abros component of the present invention
Show：
Table 1
| Alloying component | Embodiment 1 | Embodiment 2 | Embodiment 3 |
| C | 0.027 | 0.015 | 0.0097 |
| Si | 0.101 | 0.160 | 0.207 |
| Mn | 0.337 | 0.229 | 0.135 |
| P | 0.0032 | 0.0028 | 0.0034 |
| S | 0.0010 | 0.0010 | 0.0010 |
| Cr | 20.80 | 21.76 | 22.91 |
| Ni | 38.41 | 40.23 | 41.35 |
| Mo | 5.20 | 4.16 | 3.18 |
| Nb | 0.397 | 0.283 | 0.188 |
| Ti | 2.81 | 2.20 | 1.88 |
| Al | 0.45 | 0.334 | 0.553 |
| V | 0.263 | 0.162 | 0.061 |
| Cu | 3.03 | 2.01 | 1.02 |
| Zr | 0.055 | 0.079 | 0.011 |
| B | 0.0043 | 0.0031 | 0.0061 |
| Fe | Surplus | Surplus | Surplus |
Low nickel ageing strengthening sections abros of the present invention, its preparation method are as follows：
Each alloy compositions are taken according to said ratio, and vacuum induction melting is cast into pole, and electroslag remelting is into steel ingot, uniformly
Change is handled, and the Homogenization Treatments temperature is 1160~1190 DEG C, the time is 24~72 hours.Hot forging or hot rolling or hot extrusion,
Warm and hot forging temperature is 950~1150 DEG C, soaking time is 60~120 minutes；Hot-rolled temperature is 1000~1200 DEG C, soaking time
For 60~120 minutes；1000~1200 DEG C of extrusion temperature.Pipe, rod or sheet material is made in cold rolling or cold-drawn, then is heat-treated：
2~20 hours are incubated in 700~760 DEG C of air, is furnace-cooled to 620~680 DEG C with 40~60 DEG C of speed hourly, then be incubated
2~20 hours.The summation of described two soaking time sections is no less than 10 hours, and it is small that the heat treatment total time is no more than 20
When, obtain low nickel ageing strengthening sections abros of the present invention.
Embodiment 1
Using vacuum induction melting alloy 500kg, Φ 170mm pole is cast into, then electroslag remelting is into Φ 280mm steel
Ingot, steel ingot number are N73, and alloy composition is shown in Table 1.Steel ingot is placed in high temperature shaft furnace and carries out homogenization heat treatment, through forging
The pole that Φ 100mm are made is made, bar detects its tensile property, hardness after aging strengthening model, wire cutting sampling, processed sample
And ballistic work, performance are shown in Table 2, the material is used for the downhole tool of oil gas field.
Embodiment 2
Using vacuum induction melting alloy 1000kg, Φ 220mm pole is cast into, then electroslag remelting is into Φ 380mm's
Steel ingot, steel ingot number are N74, and alloy composition is shown in Table 1.Steel ingot is placed in high temperature shaft furnace and carries out homogenization heat treatment, is passed through
Jumping-up pulls out the pole for being forged into Φ 200mm, and bar detects its stretching after aging strengthening model, wire cutting sampling, processed sample
Performance, hardness and ballistic work, performance are shown in Table 2, and the material is used for the downhole tool of oil gas field.
Embodiment 3
Using vacuum induction melting alloy 3000kg, Φ 250mm pole is cast into, then electroslag remelting is into Φ 400mm's
Steel ingot, steel ingot number are N75, and alloy composition is shown in Table 1.Steel ingot is placed in high temperature shaft furnace and carries out homogenization heat treatment, is passed through
Quick forging machine jumping-up pulls out cogging, and Φ 230mm bar is made in radial forging machine forging, and bar is pressed into heavy wall through hot extrusion again
Pipe, tubing detect its tensile property, hardness and ballistic work after aging strengthening model, wire cutting sampling, processed sample, and performance is shown in Table
2, the material is used for the down-hole pipe in acid-soluble oil gas field.
Two, alloy properties
1. it is heat-treated the influence to alloy mechanical property, alloy structure
Room-temperature mechanical property of the alloy of the present invention after different heat treatment is shown in Fig. 1-Fig. 3, and alloy of the present invention makes
Aging state is generally with state, solid solution added-time effect can be used, direct aging can also be used, to obtain high obdurability.Using
The solid solution added-time imitates its metallographic structure as described in Figure 4；Using direct aging its metallographic structure as described in Figure 5.By contrast, when direct
Effect heat treatment can shorten technological process, save energy resource consumption, improve efficiency, be more recommendable handling process.
2. mechanical property tests
The mechanical property of table 2
Claims (7)
- A kind of 1. low nickel ageing strengthening sections abros, it is characterised in that the weight percentage of the alloy each component For：Ni：36.0~42.0%；Cr：19.0~25.0%；Mo：3.0~6.0%；Cu：1.0~3.50%；Ti：1.5~3.0%；Al：0.2~0.6%；Nb≤0.5%；C≤0.03%；Si≤0.5%；Mn≤0.5%；S≤0.0010；P≤0.005；Trace element 0.01~0.6%；The trace element is V, Zr, B；Fe is surplus；The alloy is made using following methods：Each alloy compositions are taken by said ratio, vacuum induction melting is cast into pole, and electroslag remelting is into steel ingot, Homogenization Treatments, The Homogenization Treatments temperature is 1160~1190 DEG C, the time is 24~72 hours；Hot forging or hot rolling or hot extrusion, cold rolling or cold Draw is into pipe, rod or sheet material, then is heat-treated：2~20 hours are incubated in 700~760 DEG C of air, it is every with 40~60 DEG C The speed of hour is furnace-cooled to 620~680 DEG C, then is incubated 2~20 hours.
- 2. alloy according to claim 1, it is characterised in that the weight percentage of the alloy each component is：Ni：38.0~42.0%；Cr：20.0~23.0%；Mo：3.0~6.0%；Cu：1.0~3.50%；Ti：1.5~3.0%；Al：0.3~0.6%；Nb≤0.5%；C≤0.03%, Si≤0.5%, Mn≤0.5%；S≤0.0010；P≤0.005；Trace element 0.01~0.6%；Fe is surplus.
- 3. alloy according to claim 1, it is characterised in that：V in the trace element：0.01~0.5%, Zr：0.01 ~0.1%, B：0.001~0.01%.
- 4. the preparation method of low nickel ageing strengthening sections abros, it is characterised in that：According to any institutes of claim 1-3 State proportioning and take each alloy compositions, vacuum induction melting is cast into pole, and electroslag remelting is described uniform into steel ingot, Homogenization Treatments Change treatment temperature is 1160~1190 DEG C, the time is 24~72 hours；Hot forging or hot rolling or hot extrusion, cold rolling or cold-drawn are made Pipe, rod or sheet material, then be heat-treated：2~20 hours are incubated in 700~760 DEG C of air, it is hourly with 40~60 DEG C Speed is furnace-cooled to 620~680 DEG C, then is incubated 2~20 hours.
- 5. according to the method for claim 4, it is characterised in that：Warm and hot forging temperature is 950~1150 DEG C, soaking time 60 ~120 minutes；Hot-rolled temperature is 1000~1200 DEG C, soaking time is 60~120 minutes；Extrusion temperature 1000~1200 ℃。
- 6. according to the method for claim 4, it is characterised in that：The summation of described two soaking time sections is small no less than 10 When.
- 7. according to the method for claim 4, it is characterised in that：The time of the heat treatment is no more than 20 hours.
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| CN105483494B (en) * | 2015-12-01 | 2018-02-06 | 重庆材料研究院有限公司 | Ageing strengthening sections abros of the easy processing into thick-wall seamless |
| CN105568113A (en) * | 2016-01-27 | 2016-05-11 | 河南工程学院 | Composite strengthening and toughening technology of high-tensile Fe-Ni-Cr-based high-temperature corrosion-resisting alloy |
| CN106086581B (en) * | 2016-08-26 | 2019-01-25 | 中国第一重型机械股份公司 | 700 DEG C of ultra supercritical unit iron nickel base alloy rotor heat treatment methods |
| CN108715951B (en) * | 2018-04-13 | 2020-06-16 | 重庆市北碚区阿尔发合金材料研究所 | Multiphase-structure nickel-chromium-iron-series high-temperature alloy and preparation method thereof |
| CN111346997A (en) * | 2020-03-25 | 2020-06-30 | 攀钢集团江油长城特殊钢有限公司 | Processing technology of shell for missile |
| CN111621674A (en) * | 2020-06-08 | 2020-09-04 | 重庆材料研究院有限公司 | Preparation method of microalloyed high-strength precise nickel-chromium resistance alloy material |
| CN112813307A (en) * | 2020-12-31 | 2021-05-18 | 江苏国镍新材料科技有限公司 | High-temperature-resistant nickel alloy and preparation method thereof |
| CN113088832A (en) * | 2021-03-26 | 2021-07-09 | 中国石油天然气集团有限公司 | Iron-nickel-based corrosion-resistant alloy continuous tube and manufacturing method thereof |
| CN113584381B (en) * | 2021-07-05 | 2023-03-07 | 重庆材料研究院有限公司 | High-strength copper-containing Ni-Fe-Cr-based age-hardening corrosion-resistant alloy and electroslag remelting method thereof |
| CN113637885B (en) * | 2021-07-19 | 2022-06-21 | 哈尔滨工程大学 | Multicomponent FeNiCoAlTiZr super elastic alloy and preparation method thereof |
| CN114150207A (en) * | 2021-10-26 | 2022-03-08 | 重庆材料研究院有限公司 | High-strength Ni-Fe-based age-hardening corrosion-resistant alloy and preparation method thereof |
| CN114107834B (en) * | 2021-11-05 | 2022-06-28 | 河钢股份有限公司 | High-strength iron-nickel-molybdenum alloy wire and low-cost preparation method thereof |
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