CN112962033A - High-strength invar alloy and processing method thereof - Google Patents
High-strength invar alloy and processing method thereof Download PDFInfo
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- CN112962033A CN112962033A CN202110136766.2A CN202110136766A CN112962033A CN 112962033 A CN112962033 A CN 112962033A CN 202110136766 A CN202110136766 A CN 202110136766A CN 112962033 A CN112962033 A CN 112962033A
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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
- C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
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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
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
Abstract
The invention provides a high-strength invar alloy which comprises the following elements in percentage by weight: 0.02-0.05% of C, less than or equal to 0.5% of Si, 0.2-0.5% of Mn, less than or equal to 0.02% of P, less than or equal to 0.005% of S, 0.3-0.8% of Mo, 35.5-36.5% of Ni, 1.3-1.7% of Al, 1.3-1.7% of Ti, and the balance of Fe and inevitable impurities. The invention also provides a preparation method of the high-strength invar alloy, which comprises smelting, forging, wire rolling, heat treatment and cold drawing. The mechanical property of the high-strength invar alloy meets the use requirement of an overhead transmission line.
Description
Technical Field
The invention relates to the technical field of high-strength alloy, in particular to a high-strength invar alloy and a processing method thereof.
Background
Because of low expansion coefficient, the invar alloy is widely applied to industries such as aviation dies, electronic information and the like, and is an indispensable material for economic construction and national defense and military industry. However, the invar alloy has low strength, so that the further expansion of the application field of the invar alloy is limited. For example, in the power industry, invar with small thermal expansion coefficient and high strength is used as the steel core of the aluminum stranded wire, so that the sag of the overhead transmission line is small, the self weight of the material is reduced, and the transmission capacity is further improved.
However, the lack of high strength invar currently hinders its further use.
Disclosure of Invention
The invention provides a high-strength invar alloy and a processing method thereof aiming at the requirements, provides the control requirements of chemical components and the processing method thereof, and has mechanical properties meeting the use requirements of overhead transmission lines.
The technical scheme of the invention is as follows:
a high-strength invar alloy comprises the following elements in percentage by weight: 0.02-0.05% of C, less than or equal to 0.5% of Si, 0.2-0.5% of Mn, less than or equal to 0.02% of P, less than or equal to 0.005% of S, 0.3-0.8% of Mo, 35.5-36.5% of Ni, 1.3-1.7% of Al, 1.3-1.7% of Ti, and the balance of Fe and inevitable impurities.
Optionally, the content of Al and Ti satisfies that Al + Ti is more than or equal to 2.8%.
Optionally, the content of Al and Ti satisfies that Al/Ti is 0.8-1.2.
Alternatively, the contents of Mo and C satisfy Mo/(10 XC) ≧ 1.
Optionally, the tensile strength of the high-strength invar alloy is more than or equal to 1300MPa, and the elongation after fracture is more than or equal to 3%.
Optionally, the linear expansion coefficient alpha of the high-strength invar alloy at 20-230 ℃ is less than or equal to 3.0 multiplied by 10-6(1/DEG C), the linear expansion coefficient alpha is less than or equal to 10.8 multiplied by 10 at the temperature of 230-290 DEG C-6(1/℃)。
A method for preparing a high strength invar alloy, comprising: smelting, forging, rolling wire rods, performing heat treatment and cold drawing, wherein in the forging step, the heating temperature of a blank is controlled to be 1130-1160 ℃, and the finish forging temperature is more than or equal to 850 ℃.
Optionally, in the wire rolling step, the heating temperature of the blank is controlled to be 1130-1160 ℃, the spinning temperature is more than or equal to 900 ℃, and water is passed through for cooling, so that the rolled wire is obtained.
Optionally, in the heat treatment step, the rolled wire rod is subjected to solution heat treatment and aging heat treatment;
wherein, when the solution heat treatment is carried out, the temperature of the solution heat treatment is 1020-1100 ℃, the heat preservation time is 25-40 min, and then water cooling is carried out; and (3) during aging heat treatment, the aging temperature is 700-800 ℃, the heat preservation time is 4-8 h, and then water cooling is carried out.
Optionally, in the cold drawing step, the cold drawing deformation amount is greater than 50%.
Compared with the prior art, the high-strength invar alloy and the processing method thereof have the following beneficial effects that:
the invention optimizes and adjusts the composition and the proportion of the elements of the invar alloy, so that the elements generate a coordination effect. The invention optimizes the technological parameters of the processing method of the high-strength invar alloy. Through the combined action of the element composition, the proportion and the processing method, the strength of the invar alloy is greatly improved, and the mechanical property of the invar alloy meets the use requirement of an overhead transmission line.
Detailed Description
The present invention will be described in further detail below with reference to specific embodiments, but it should be understood that the method of the present invention is not limited thereto.
Unless otherwise indicated, the methods of the present invention employ methods and apparatus conventional in the art, except as described below.
Unless otherwise defined, technical terms referred to in the present invention have meanings commonly understood by those skilled in the art.
In one aspect, the invention provides a high strength invar alloy comprising the following elements in weight percent: 0.02-0.05% of C, less than or equal to 0.5% of Si, 0.2-0.5% of Mn, less than or equal to 0.02% of P, less than or equal to 0.005% of S, 0.3-0.8% of Mo, 35.5-36.5% of Ni, 1.3-1.7% of Al, 1.3-1.7% of Ti, and the balance of Fe and inevitable impurities. Preferably, the content of Al and Ti satisfies that Al + Ti is more than or equal to 2.8%, and Al/Ti is 0.8-1.2; preferably, the content of Mo and C satisfies Mo/(10 XC) ≥ 1.
The invention optimizes and adjusts the composition and the proportion of invar alloy elements to generate a coordination effect among the elements, and the method specifically comprises the following steps:
c mainly plays a role in solid solution strengthening. When the C content is too low (i.e., less than 0.02%), the strengthening effect is insignificant. However, if the content of C added is too high (i.e., more than 0.05%), C combines with Ti element in the alloy to form a large amount of primary TiC precipitates, thereby deteriorating the performance. Therefore, the content of C is controlled to be 0.02-0.05%.
Si is a harmful element in the alloy, and can promote the precipitation of harmful phases. When the Si content is more than 0.5%, a Si-containing harmful precipitate phase is precipitated at grain boundaries, thereby weakening the strength of the grain boundaries, resulting in cracking. Therefore, the Si content is controlled to be less than or equal to 0.5 percent.
The proper addition of Mn plays a role in solid solution strengthening and simultaneously improves the appearance of inclusions. When the Mn content is too low (i.e., less than 0.2%), the strengthening effect is insignificant. However, the addition of Mn in an excessively high amount (i.e., more than 0.5%) causes the alloy to have reduced thermoplasticity, thereby causing forging cracks. Therefore, the Mn content is controlled to be 0.2-0.5%.
Ni is the main alloying element of the alloy and plays a role in adjusting the thermal expansion coefficient. The lowest level of thermal expansion coefficient of the alloy is achieved only when the Ni content is close to 36%. Therefore, the Ni content is controlled to be 35.5-36.5%.
Mo is a solid solution strengthening element and is added in a proper amount. However, when it is less than 0.3%, the solid solution strengthening effect is not significant, and when it is more than 0.8%, the cost increases and some carbides of Mo are formed, affecting the workability. Therefore, the content of Mo is controlled to be 0.3-0.8%.
Al and Ti are the most important alloying elements, and are added simultaneously, so that a large amount of Ni3AlTi nano-scale precipitates can be formed during later aging heat treatment of the alloy, and the strength is obviously improved. Al + Ti in the alloy is more than or equal to 2.8 percent so as to meet the requirement of precipitates with certain volume fractions. Al/Ti is 0.8-1.2 to prevent the morphology of the precipitates from changing, thereby reducing the strength of the precipitates.
The content of Mo and C meets the condition that Mo/(10 XC) is more than or equal to 1, a small amount of nano-scale MoC precipitates can be formed, and the auxiliary precipitation strengthening effect is achieved.
In another aspect, the present invention provides a method for preparing a high strength invar alloy, comprising: smelting, forging, wire rolling, heat treatment and cold drawing.
Specifically, the preparation method of the high-strength invar alloy comprises the following steps:
(1) smelting
The smelting can adopt the conventional method in the field, and the technicians in the field can reasonably select the specific process steps and parameters according to the actual conditions, which is not described herein.
(2) Forging
The heating temperature of the blank is controlled to be 1130-1160 ℃, and the finish forging temperature is more than or equal to 850 ℃.
(3) Wire rod rolling
Rolling the forged billet into a wire rod. And during rolling, controlling the heating temperature of the blank to be 1130-1160 ℃, controlling the spinning temperature to be more than or equal to 900 ℃, and cooling through water to obtain a rolled wire.
(4) Thermal treatment
And carrying out solid solution and aging heat treatment on the rolled wire.
When the solution heat treatment is carried out, the temperature of the solution heat treatment is 1020-1100 ℃, the heat preservation time is 25-40 min, and then water cooling is carried out; and (3) during aging heat treatment, the aging temperature is 700-800 ℃, the heat preservation time is 4-8 h, and then water cooling is carried out.
(5) Cold drawing
In the cold drawing step, the cold drawing deformation amount needs to be more than 50%.
In the preparation method of the high-strength invar alloy, except the process steps and the parameters, the rest are conventional methods and parameters, and the specific process steps and the parameters can be reasonably selected by a person skilled in the art according to actual needs, and are not described herein any more.
The inventor finds that the alloy has high thermoplasticity in the range of 1130-1160 ℃, and when the temperature is higher than 1160 ℃, the thermoplasticity is reduced, and the alloy is easy to crack when being forged. The temperature of the solution heat treatment is 1020-1100 ℃, and in the interval, the static recrystallization of the structure of the alloy is complete and the structure is uniform. The aging temperature is 700-800 ℃, in the temperature range, precipitates have the highest volume fraction, the sizes of the precipitates are all nano-scale, and the precipitation strengthening effect is obvious.
After cold drawing, the performance of the invar alloy:
the tensile strength is more than or equal to 1300Mpa, and the elongation after fracture is more than or equal to 3 percent;
linear expansion coefficient alpha is less than or equal to 3.0 multiplied by 10 at the temperature of 20-230 DEG C-6(1/℃)；
The linear expansion coefficient alpha of 230-290 ℃ is less than or equal to 10.8 multiplied by 10-6(1/℃)。
Examples
The invention is further illustrated by the following examples, which are not intended to limit the scope of the invention. The experimental methods without specifying specific conditions in the following examples were selected according to the conventional methods and conditions, or according to the commercial instructions.
In the following examples, the detection method of each parameter is as follows:
tensile strength: ASTM A370
Elongation after fracture: ASTM A370
Linear expansion coefficient α at 20-230 ℃: GB/T4339
Linear expansion coefficient α at 230-290 ℃: GB/T4339
Table 1, unit: by weight%
Example one
The actual composition is shown in table 1 above. The billet is forged, and the billet heating temperature is 1140 ℃, and the finish forging temperature is 870 ℃. And grinding the forged blank to ensure that no visible defects exist. Rolling the wire rod, wherein the blank heating temperature is 1150 ℃, the spinning temperature is 930 ℃, and water cooling is carried out. And carrying out solid solution and aging heat treatment on the rolled wire, wherein the temperature of the solid solution heat treatment is 1040 ℃, the heat preservation time is 30min, and water cooling is carried out. The aging temperature is 720 ℃, the heat preservation time is 4 hours, and the water cooling is carried out. And (3) carrying out acid pickling and cold drawing on the wire, wherein the cold drawing deformation is more than 50%. Performance after cold drawing:
the tensile strength is 1340Mpa, and the elongation after fracture is 3.5%.
Linear expansion coefficient alpha of 2.8 x 10 at 20-230 deg.C-6(1/℃)
230-290 ℃ linear expansion coefficient alpha is 9.9 multiplied by 10-6(1/℃)
Example two
The actual composition is shown in table 1 above. Forging the blank, wherein the heating temperature of the blank is 1150 ℃, and the finish forging temperature is 880 ℃. And grinding the forged blank to ensure that no visible defects exist. Rolling the wire rod, heating the blank at 1140 deg.C, spinning at 950 deg.C, and cooling with water. And carrying out solid solution and aging heat treatment on the rolled wire, wherein the temperature of the solid solution heat treatment is 1050 ℃, the heat preservation time is 35min, and water cooling is carried out. The aging temperature is 740 ℃, the heat preservation time is 5h, and the water cooling is carried out. And (3) carrying out acid pickling and cold drawing on the wire, wherein the cold drawing deformation is more than 50%. Performance after cold drawing:
tensile strength is 1350Mpa, and elongation after fracture is 3.2%.
Linear expansion coefficient alpha of 2.7 x 10 at 20-230 deg.C-6(1/℃)
230-290 ℃ linear expansion coefficient alpha is 10.5 multiplied by 10-6(1/℃)
EXAMPLE III
The actual composition is shown in table 1 above. And forging the blank, wherein the blank heating temperature is 1140 ℃, and the finish forging temperature is 860 ℃. And grinding the forged blank to ensure that no visible defects exist. Rolling the wire rod, wherein the blank heating temperature is 1150 ℃, the spinning temperature is 970 ℃, and the wire rod is cooled by water. And carrying out solid solution and aging heat treatment on the rolled wire, wherein the temperature of the solid solution heat treatment is 1040 ℃, the heat preservation time is 30min, and water cooling is carried out. The aging temperature is 730 ℃, the heat preservation time is 4 hours, and the water cooling is carried out. And (3) carrying out acid pickling and cold drawing on the wire, wherein the cold drawing deformation is more than 50%. Performance after cold drawing:
the tensile strength is 1340Mpa, and the elongation after fracture is 3.4%.
Linear expansion coefficient alpha of 2.8 x 10 at 20-230 deg.C-6(1/℃)
230-290 ℃ linear expansion coefficient alpha is 10.2 multiplied by 10-6(1/℃)
The above embodiments are preferred embodiments of the present invention, but the present invention is not limited to the above embodiments, and any other substitutions, modifications, combinations, changes, simplifications, etc., which are made without departing from the spirit and principle of the present invention, should be construed as equivalents and included in the protection scope of the present invention.
Claims (10)
1. A high-strength invar alloy is characterized by comprising the following elements in percentage by weight: 0.02-0.05% of C, less than or equal to 0.5% of Si, 0.2-0.5% of Mn, less than or equal to 0.02% of P, less than or equal to 0.005% of S, 0.3-0.8% of Mo, 35.5-36.5% of Ni, 1.3-1.7% of Al, 1.3-1.7% of Ti, and the balance of Fe and inevitable impurities.
2. The high strength invar alloy of claim 1, wherein the Al and Ti content is such that Al + Ti is greater than or equal to 2.8%.
3. The high strength invar alloy according to claim 1, wherein the Al and Ti contents satisfy Al/Ti of 0.8 to 1.2.
4. The high strength invar alloy of claim 1, wherein the contents of Mo and C satisfy Mo/(10 xc) ≥ 1.
5. The high strength invar alloy of claim 1, wherein the high strength invar alloy has a tensile strength of not less than 1300Mpa and an elongation after fracture of not less than 3%.
6. The high strength invar alloy of claim 1 having a linear expansion coefficient α ≦ 3.0 x 10 for 20-230 ℃-6(1/DEG C), the linear expansion coefficient alpha is less than or equal to 10.8 multiplied by 10 at the temperature of 230-290 DEG C-6(1/℃)。
7. The method of making the high strength invar alloy of any of claims 1-6, comprising: smelting, forging, rolling wire rods, performing heat treatment and cold drawing, and is characterized in that in the forging step, the heating temperature of a blank is controlled to be 1130-1160 ℃, and the finish forging temperature is more than or equal to 850 ℃.
8. The preparation method according to claim 7, wherein in the wire rolling step, the blank heating temperature is controlled to be 1130-1160 ℃, the spinning temperature is not less than 900 ℃, and water is passed through for cooling, so as to obtain the rolled wire.
9. The production method according to claim 7, wherein in the heat treatment step, the rolled wire rod is subjected to solution heat treatment and aging heat treatment;
wherein, when the solution heat treatment is carried out, the temperature of the solution heat treatment is 1020-1100 ℃, the heat preservation time is 25-40 min, and then water cooling is carried out; and (3) during aging heat treatment, the aging temperature is 700-800 ℃, the heat preservation time is 4-8 h, and then water cooling is carried out.
10. The production method according to claim 7, wherein in the cold drawing step, the cold drawing deformation amount is more than 50%.
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| 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 |
| CN115161444A (en) * | 2022-08-12 | 2022-10-11 | 山西太钢不锈钢精密带钢有限公司 | Low-expansion alloy 4J36 precision foil and superfine crystal solid solution heat treatment method and application thereof |
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| CN115161444A (en) * | 2022-08-12 | 2022-10-11 | 山西太钢不锈钢精密带钢有限公司 | Low-expansion alloy 4J36 precision foil and superfine crystal solid solution heat treatment method and application thereof |
| CN115161444B (en) * | 2022-08-12 | 2024-01-19 | 山西太钢不锈钢精密带钢有限公司 | Low-expansion alloy 4J36 precise foil and superfine crystal solid solution heat treatment method and application thereof |
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