CN114959214A - Homogenization treatment method of niobium-containing austenitic stainless steel - Google Patents

Homogenization treatment method of niobium-containing austenitic stainless steel Download PDF

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Publication number
CN114959214A
CN114959214A CN202210552972.6A CN202210552972A CN114959214A CN 114959214 A CN114959214 A CN 114959214A CN 202210552972 A CN202210552972 A CN 202210552972A CN 114959214 A CN114959214 A CN 114959214A
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stainless steel
niobium
austenitic stainless
equal
containing austenitic
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Inventor
陈胜虎
徐海涛
戎利建
燕春光
谢昂
刘新鹏
姜海昌
庄毅
杨红义
李依依
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Institute of Metal Research of CAS
China Institute of Atomic of Energy
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Institute of Metal Research of CAS
China Institute of Atomic of Energy
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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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/004—Heat treatment of ferrous alloys containing Cr and Ni
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/005—Heat treatment of ferrous alloys containing Mn
    • 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
    • C21D6/00—Heat treatment of ferrous alloys
    • C21D6/008—Heat treatment of ferrous alloys containing Si
    • 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
    • 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
    • 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
    • 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
    • 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
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • 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
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/001—Austenite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

Abstract

The invention discloses a homogenization treatment method of niobium-containing austenitic stainless steel, and belongs to the technical field of austenitic stainless steel. The niobium-containing austenitic stainless steel applicable to the invention comprises the following chemical components: nb: 0.4-1.5%; c: 0.04-0.15%; Nb/C is more than or equal to 8; ni: 8.0-15.0%; cr: 16.0-20.0%; mn is less than or equal to 2.0 percent; si is less than or equal to 1.0 percent; mo is less than or equal to 3.0 percent; fe and inevitable residual elements as the balance. Putting the ingot or the casting blank into a heating furnace, wherein the charging temperature is less than 700 ℃, then heating to 1240 and 1260 ℃, and the heat preservation time is more than or equal to 20 h. After the homogenization treatment, the mixture is directly processed by heat or cooled to 850-950 ℃ with a furnace and then cooled by air. The invention can synchronously improve the form of primary niobium carbide in the casting blank, eliminate delta ferrite, improve the thermoplasticity of the niobium-containing austenitic stainless steel and provide high-quality cast ingots or casting blanks for preparing products such as high-performance niobium-containing austenitic stainless steel forgings, plates, pipes and the like.

Description

Homogenization treatment method of niobium-containing austenitic stainless steel
The technical field is as follows:
the invention relates to the technical field of austenitic stainless steel, in particular to a homogenization treatment method of niobium-containing austenitic stainless steel.
Background art:
the austenitic stainless steel is widely applied to the fields of petrochemical industry, thermal power, nuclear power and the like due to excellent room-temperature and medium-temperature mechanical properties, corrosion resistance, forming property and welding process property. Based on the austenitic stainless steel, a certain content of Nb element is added, and the stabilized austenitic stainless steel is further developed, such as the austenitic stainless steel of 347, 348, 316Nb, 309Nb, 310Nb and the like. The addition of Nb fixes carbon element in steel in niobium carbide, which can improve intercrystalline corrosion performance. Meanwhile, nano-sized niobium carbide is precipitated in the austenite matrix, so that the high-temperature strength, the durability and the anti-irradiation performance can be obviously improved. The relevant performance of the stabilized austenitic stainless steel is closely related to the size and distribution of niobium carbide, and in order to improve the size and distribution of the niobium carbide, scientific researchers provide various methods, such as heat treatment regulation, mechanical heat treatment process, cold deformation treatment and the like.
For the stabilized austenitic stainless steel with the Nb content being more than or equal to 0.3 wt%, primary niobium carbide can be formed in the solidification process, and the quantity of the primary niobium carbide is increased along with the increase of the Nb content, and even the primary niobium carbide is distributed in a continuous net shape. On the one hand, the coarse primary niobium carbide can reduce the thermoplasticity of the alloy, and the cracking phenomenon can be caused in the later hot working process. On the other hand, the primary niobium carbide has small contribution to the strength, but is easy to become a crack source in the deformation process, and the mechanical property is greatly reduced. The formation of primary niobium carbide also consumes a large amount of Nb element, which is not beneficial to the precipitation control of secondary niobium carbide in the later period. Therefore, how to improve the morphology of the primary niobium carbide in the cast sample is beneficial to improving the hot workability of the alloy and the precipitation control of the high-density fine niobium carbide. In addition, in austenitic stainless steel, δ ferrite remaining to room temperature due to peritectic reaction or solidification segregation is likely to occur during solidification, and Nb promotes the formation of δ ferrite as a ferrite-forming element. In the high-temperature long-term service process, delta ferrite is easily decomposed into brittle phases such as sigma and chi, and the toughness of the alloy is greatly damaged. Therefore, elimination of δ ferrite in the as-cast sample will also contribute to the improvement of the performance.
The invention content is as follows:
aiming at the problem that coarse primary niobium carbide and delta ferrite appear in a cast sample of niobium-containing austenitic stainless steel, the invention aims to provide a homogenization treatment method of niobium-containing austenitic stainless steel, which can synchronously realize the purposes of refining the primary niobium carbide and eliminating the delta ferrite.
In order to achieve the purpose, the technical scheme of the invention is as follows:
a homogenization treatment method of niobium-containing austenitic stainless steel is applicable to the chemical components of the niobium-containing austenitic stainless steel, and the chemical components of the austenitic stainless steel in percentage by weight are as follows:
nb: 0.4 to 1.5 percent; c: 0.04-0.15%; Nb/C is more than or equal to 8; ni: 8.0-15.0%; cr: 16.0-20.0%; mn is less than or equal to 2.0 percent; si is less than or equal to 1.0 percent; mo is less than or equal to 3.0 percent; fe and inevitable residual elements as the balance. Wherein, in the niobium-containing austenitic stainless steel, the content of Nb is 0.4-1.5 wt.%; c content is 0.04-0.15 wt.%.
The homogenization treatment method of the niobium-containing austenitic stainless steel specifically comprises the following steps:
(1) putting the ingot or the casting blank into a heating furnace, wherein the charging temperature is less than 700 ℃, then heating to 1200-1260 ℃, and the heat preservation time is more than or equal to 10 h.
(2) After the homogenization treatment is finished, directly carrying out hot working or cooling with a furnace to a certain temperature and then air cooling.
It is preferable that the homogenization temperature is 1240-1260 ℃ in step (1).
Preferably, in step (1), the homogenization incubation time is not less than 20 h.
Preferably, in step (2), after the homogenization treatment is finished, the hot working is directly performed or the furnace cooling is performed to 850-.
The invention has the advantages and beneficial effects that:
1. the invention can effectively eliminate the delta ferrite in the casting blank and avoid the influence of the delta ferrite on the obdurability.
2. The invention can improve the form of primary niobium carbide in a casting blank, obviously improve the thermoplasticity of the niobium-containing austenitic stainless steel, and simultaneously obviously reduce the influence of coarse primary niobium carbide on the mechanical property.
3. According to the invention, by controlling the cooling process after homogenization and heat preservation, the problem of precipitation of brittle intermetallic compounds in the cooling process can be avoided.
4. The application of the invention provides high-quality cast ingots or casting blanks for the preparation of products such as high-performance niobium-containing austenitic stainless steel forgings, plates, pipes and the like.
Description of the drawings:
FIG. 1 is a metallographic photograph of an ingot of austenitic stainless steel containing niobium in example 1.
FIG. 2 is a metallographic photograph of a cast slab after the homogenization treatment in example 1.
FIG. 3 is a metallographic photograph of an ingot of austenitic stainless steel containing niobium in example 2.
FIG. 4 is a metallographic photograph of a cast slab after the homogenization treatment in example 2.
FIG. 5 is a metallographic photograph of an ingot obtained by the homogenization treatment in comparative example 1.
FIG. 6 is a metallographic photograph of an ingot obtained by the homogenization treatment in comparative example 2.
FIG. 7 is a metallographic photograph of an ingot obtained by the homogenization treatment in comparative example 3.
The specific implementation mode is as follows:
the method of homogenizing an austenitic stainless steel containing niobium according to the present invention will be further described with reference to examples.
The mass percentages of chemical components of the niobium-containing austenitic stainless steel in the embodiment of the invention are shown in table 1, refining equipment is adopted to ensure that the chemical components of molten steel meet the component control requirements, then the molten steel is cast into an ingot, and a full-thickness sample is taken from the cooled ingot for homogenization treatment.
TABLE 1 alloy chemistry (wt.%)
C Nb Ni Cr Mn Mo P S
Practice ofExample 1 0.071 0.70 10.52 17.62 1.52 0.15 0.006 0.0020
Example 2 0.10 0.94 10.80 16.88 1.49 0.32 0.007 0.0021
Example 1:
the metallographic structure of the austenitic stainless steel ingot containing niobium in the present example is shown in fig. 1, a skeletal primary niobium carbide is formed, a part of the primary niobium carbide is continuously distributed, and a small amount of granular δ ferrite is observed.
Putting the cast ingot into a heating furnace, heating to 1250 ℃, preserving heat for 12 hours, cooling to 900 ℃ along with the furnace, discharging and air cooling. The typical metallographic structure after the homogenization treatment is shown in fig. 2, the primary niobium carbide is spherical or ellipsoidal and is distributed discontinuously, and the form of the primary niobium carbide is obviously improved; meanwhile, the casting blank does not contain delta ferrite.
Example 2:
the metallographic structure of the austenitic stainless steel ingot containing niobium in the present example is shown in fig. 3, a skeletal primary niobium carbide is formed, a part of the primary niobium carbide is continuously distributed, and a small amount of granular δ ferrite is observed.
Putting the cast ingot into a heating furnace, heating to 1250 ℃, preserving heat for 12 hours, cooling to 900 ℃ along with the furnace, discharging and air cooling. The typical metallographic structure after the homogenization treatment is shown in fig. 4, the primary niobium carbide is spherical or ellipsoidal and is distributed discontinuously, and the form of the primary niobium carbide is improved remarkably; while containing no delta ferrite.
Comparative example 1:
the same ingot as in example 2 was used, and the ingot was placed in a heating furnace at a charging temperature of less than 700 ℃, then heated to 1100 ℃, heat-preserved for 12 hours, cooled to 900 ℃ with the furnace, and then taken out of the furnace for air cooling. The typical metallographic structure after the homogenization treatment is shown in fig. 5, the cast ingot does not contain delta ferrite, however, the primary niobium carbide has a similar size and distribution to the cast sample (see fig. 3), the form is still skeleton, part of the primary niobium carbide is distributed continuously, and more precipitated phases exist in the crystal. Therefore, the purpose of refining the primary niobium carbide cannot be achieved by adopting a lower homogenization temperature.
Comparative example 2:
the same ingot as in example 2 was used, and the ingot was placed in a heating furnace at a charging temperature of less than 700 ℃, then heated to 1150 ℃, heat-preserved for 12 hours, cooled to 900 ℃ with the furnace, and then taken out of the furnace for air cooling. The typical metallographic structure after the homogenization treatment is shown in fig. 6, the cast ingot does not contain delta ferrite, however, the primary niobium carbide has a similar size and distribution to the cast sample (see fig. 3), the form is still skeleton, part of the primary niobium carbide is distributed continuously, and more precipitated phases exist in the crystal. Therefore, the purpose of refining the primary niobium carbide cannot be achieved by adopting a lower homogenization temperature.
Comparative example 3:
the same ingot as in example 2 was used, and the ingot was placed in a heating furnace at a charging temperature of less than 700 ℃, subsequently heated to 1250 ℃, heat-preserved for 5 hours, cooled to 900 ℃ with the furnace, and then taken out of the furnace for air cooling. The typical metallographic structure after the homogenization treatment is shown in fig. 7, the cast ingot does not contain delta ferrite, however, the primary niobium carbide has a size and distribution similar to those of the cast sample (see fig. 3), the form is still skeleton, and part of the primary niobium carbide is continuously distributed. Therefore, the purpose of refining the primary niobium carbide cannot be achieved by adopting shorter homogenization heat preservation time.
The above embodiments are only for illustrating the technical concept and features of the present invention, and are intended to enable those skilled in the art to understand the contents of the present invention and implement the present invention, and not to limit the protection scope of the present invention. Besides the above embodiments, there may be variations in the chemical composition of the materials, etc., and such equivalents should also be considered within the scope of protection.

Claims (7)

1. A homogenization treatment method of niobium-containing austenitic stainless steel is characterized in that: the method comprises the following steps:
1) homogenizing: putting the niobium-containing austenitic stainless steel ingot or casting blank into a heating furnace, wherein the charging temperature is less than 700 ℃, then heating to 1200-1260 ℃, and the heat preservation time is more than or equal to 10 hours;
2) after the homogenization treatment is finished, directly carrying out hot working or cooling with a furnace to a certain temperature and then air cooling.
2. The method for homogenizing a niobium-containing austenitic stainless steel as set forth in claim 1, wherein: the homogenization temperature in step 1) is 1240-1260 ℃.
3. The method for homogenizing an austenitic stainless steel containing niobium according to claim 1, wherein: the homogenization heat preservation time in the step 1) is more than or equal to 20 hours.
4. The method for homogenizing a niobium-containing austenitic stainless steel as set forth in claim 1, wherein: in the step 2), after the homogenization treatment is finished, the hot working is directly carried out or the furnace cooling is carried out to 850-950 ℃ and then the air cooling is carried out.
5. The method for homogenizing a niobium-containing austenitic stainless steel as set forth in claim 1, wherein: the niobium-containing austenitic stainless steel comprises the following chemical components in percentage by weight: Nb/C is more than or equal to 8; ni: 8.0-15.0%; cr: 16.0-20.0%; mn is less than or equal to 2.0 percent; si is less than or equal to 1.0 percent; mo is less than or equal to 3.0 percent; fe and inevitable residual elements as the balance.
6. The method for homogenizing a niobium-containing austenitic stainless steel as set forth in claim 1, wherein: according to weight percentage, in the austenitic stainless steel containing niobium, the ratio of Nb: 0.4-1.5%; c: 0.04-0.15 percent.
7. The method for homogenizing a niobium-containing austenitic stainless steel as set forth in claim 1, wherein: the method can synchronously improve the form of primary niobium carbide and eliminate delta ferrite.
CN202210552972.6A 2022-05-19 2022-05-19 Homogenization treatment method of niobium-containing austenitic stainless steel Pending CN114959214A (en)

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Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106893831A (en) * 2017-03-13 2017-06-27 东北大学 A kind of super austenitic stainless steel high temperature homogenization processing method
KR20190016629A (en) * 2017-08-08 2019-02-19 한국기계연구원 Austenitic heat resisting steel and method of manufacuring the same
CN112143973A (en) * 2020-09-25 2020-12-29 山西太钢不锈钢股份有限公司 High-strength high-corrosion-resistance super austenitic stainless steel and preparation method thereof
CN112410517A (en) * 2020-11-18 2021-02-26 中国科学院金属研究所 Method for eliminating delta ferrite in austenitic stainless steel
CN113564461A (en) * 2021-06-29 2021-10-29 鞍钢股份有限公司 Austenitic stainless steel plate for fast neutron reactor and manufacturing method thereof
US20210348248A1 (en) * 2018-11-13 2021-11-11 Korea Advanced Institute Of Science And Technology Austenitic stainless steel containing niobium and manufacturing method of the same
CN114341389A (en) * 2019-11-18 2022-04-12 韩国科学技术院 Austenitic stainless steel having a large amount of uniformly distributed nano-sized precipitates and method for preparing the same

Patent Citations (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN106893831A (en) * 2017-03-13 2017-06-27 东北大学 A kind of super austenitic stainless steel high temperature homogenization processing method
KR20190016629A (en) * 2017-08-08 2019-02-19 한국기계연구원 Austenitic heat resisting steel and method of manufacuring the same
US20210348248A1 (en) * 2018-11-13 2021-11-11 Korea Advanced Institute Of Science And Technology Austenitic stainless steel containing niobium and manufacturing method of the same
CN114341389A (en) * 2019-11-18 2022-04-12 韩国科学技术院 Austenitic stainless steel having a large amount of uniformly distributed nano-sized precipitates and method for preparing the same
CN112143973A (en) * 2020-09-25 2020-12-29 山西太钢不锈钢股份有限公司 High-strength high-corrosion-resistance super austenitic stainless steel and preparation method thereof
CN112410517A (en) * 2020-11-18 2021-02-26 中国科学院金属研究所 Method for eliminating delta ferrite in austenitic stainless steel
CN113564461A (en) * 2021-06-29 2021-10-29 鞍钢股份有限公司 Austenitic stainless steel plate for fast neutron reactor and manufacturing method thereof

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