CN113957335B - Production and preparation method of non-quenched and tempered steel with tensile strength of 1100MPa - Google Patents
Production and preparation method of non-quenched and tempered steel with tensile strength of 1100MPa Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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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
- C22C38/06—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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- 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 production and preparation method of non-quenched and tempered steel with tensile strength of 1100MPa, which comprises a steel-making process and a steel rolling process, and simultaneously limits the chemical components to be as follows by mass percent: c:0.28% -0.30%, si: 0.94-1.23%, mn: 1.80-1.86%, P is less than or equal to 0.025%, S is less than or equal to 0.020%, V: 0.13-0.15%, cr: 0.56-0.60%, ti:0.09% -0.10%, al:0.06 percent to 0.07 percent; nb:0.05 to 0.07 percent; RE: 0.0010-0.0020%, N:0.0170 to 0.0200 percent, and the balance of Fe and other trace impurity elements. The invention has simple chemical components, and has the advantages of simple control, low manufacturing cost, strong operability and the like aiming at the production of 1100 MPa-grade non-quenched and tempered steel.
Description
Technical Field
The invention relates to the field of material metallurgy, in particular to a production and preparation method of non-quenched and tempered steel with the tensile strength of 1100 MPa.
Background
In the machine manufacturing industry of automobiles and the like, a large amount of alloy structural steel and carbon structural steel are used for manufacturing machine parts. Generally, when high strength, high toughness, good structural integrity and excellent fatigue properties are the main requirements, these excellent properties are usually obtained by forming these mechanical parts by a forging process and then by appropriate heat treatment such as quenching and high temperature tempering (thermal refining) to obtain fine tempered martensite. The thermal refining generally comprises the following three heat treatment processes: heating to austenitize after forging, quenching treatment and high-temperature tempering treatment. These heat treatment processes not only consume much energy and time, but also pollute the environment and increase the manufacturing cost of the parts.
Since the end of the 20 th 70 s, research and development work for eliminating or simplifying the thermal refining process after forging has been conducted in various countries all over the world in order to save energy, protect the environment and reduce the manufacturing cost. In particular, since the first microalloy non-quenched and tempered steel 49MnVS3 in the world is successfully developed in Gerlach company of Germany, ferrite-pearlite type microalloy non-quenched and tempered steel is increasingly used for manufacturing automobile forgings such as crankshafts, connecting rods and the like. However, the yield strength and toughness of ferrite + pearlite type microalloy non-quenched and tempered steel using the precipitation strengthening mechanism are generally lower than those of quenched and tempered steel of the same strength level, which also limits the range of applications. Therefore, for high stress safety parts such as automobile front axles and steering arms, which require high strength and , bainite non-heat treated steel is increasingly used instead of heat treated steel.
In reported documents and patents, the tensile strength of non-quenched and tempered steel reaches 1100MPa, and a high-carbon design is adopted, so that the non-quenched and tempered steel does not have good enough toughness.
Disclosure of Invention
In order to solve the technical problems, the invention aims to provide a production method of non-quenched and tempered steel with the tensile strength of 1100 MPa.
The non-quenched and tempered steel has the technical index R p0.2 ≥800MPa；R m More than or equal to 1100MPa; a is more than or equal to 5 percent; the hardness is more than or equal to 360HB; k is (V)2 ≥12J；K (U)2 ≥30J。
In order to solve the technical problem, the invention adopts the following technical scheme:
the invention relates to a production and preparation method of non-quenched and tempered steel with tensile strength of 1100MPa, which comprises the following steel-making process: converter-external refining-VD vacuum treatment-continuous casting blank, performing Ar blowing operation in the whole process, performing desulfurization according to the components and temperature of molten steel in the converter, performing component fine adjustment and heating operation, wherein the deep vacuum time is more than or equal to 13min, ensuring that the soft blowing time is more than 18min, preventing the molten steel from being exposed during soft blowing, and performing constant-pulling-speed operation at the superheat degree of less than or equal to 30 ℃.
The steel rolling process flow comprises the following steps: heating a casting blank, removing phosphorus by high-pressure water, cogging in a phi 850mm cogging mill, rolling in a phi 700mm multiplied by 3+ phi 550mm multiplied by 4 continuous rolling mill, sawing, slow cooling, nondestructive testing, stacking, checking, grinding, bundling, warehousing and delivering; the technical parameters controlled in the rolling process are as follows:
the heating temperature is 1150-1200 ℃, and the heat preservation time is more than or equal to 3 hours;
the initial rolling temperature is less than or equal to 1050 ℃;
the finishing temperature is less than or equal to 870 ℃;
the slow cooling temperature is more than or equal to 450 ℃;
the slow cooling time is more than or equal to 48 hours.
Further, the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28% -0.30%, si: 0.94-1.23%, mn: 1.80-1.86%, P is less than or equal to 0.025%, S is less than or equal to 0.020%, V: 0.13-0.15%, cr: 0.56-0.60%, ti:0.09% -0.10%, al:0.06 percent to 0.07 percent; nb:0.05 percent to 0.07 percent; RE: 0.0010-0.0020%, N: 0.0170-0.0200% of Fe and other trace impurity elements.
Further, the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28%, si:0.94%, mn:1.81%, P:0.019%, S:0.09%, V:0.14%, cr:0.56%, ti:0.10%, al:0.06 percent; nb:0.06 percent; RE:0.0012%, N:0.0170 percent, and the balance of Fe and other trace impurity elements.
Further, the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.29%, si:0.95%, mn:1.83%, P:0.019%, S:0.08%, V:0.15%, cr:0.56%, ti:0.09%, al:0.07 percent; nb:0.05 percent; RE:0.0015%, N:0.0175 percent, and the balance of Fe and other trace impurity elements.
Further, the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28%, si:0.95%, mn:1.82%, P:0.020%, S:0.09%, V:0.14%, cr:0.58%, ti:0.10%, al:0.06 percent; nb:0.05 percent; RE:0.0015%, N:0.0180 percent, and the balance of Fe and other trace impurity elements.
The effects of some elements in the steel of the invention are as follows:
the C element is the most effective strengthening element in the steel, and the increase of the C content in the steel can improve the strength but reduce the toughness; by applying the technology of the invention, the upper limit of the carbon content is between 0.28 and 0.43 percent under the condition of not influencing the toughness of the steel.
The Mn element is used as an element for expanding an austenite phase region, is favorable for forming a pearlite structure, reduces the interlamellar spacing of pearlite plates and improves the strength of non-quenched and tempered steel, and is controlled to be 1.80-1.86%.
Si is an advantageous element for solid solution strengthening and deoxidation, and also an advantageous element for improving hardenability. Si can also delay high-temperature softening and increase high-temperature strength, and the Si element is controlled to be 0.94-1.23%.
P, S: p and S are impurity elements in the steel. P has a certain effect of improving corrosion resistance, but is an element easy to segregate, generates serious segregation in the local part of steel, reduces plasticity and toughness, and is extremely harmful to low-temperature toughness. The S element is easy to segregate and enrich in the steel and is an element harmful to the corrosion resistance, but the S element has better free-cutting performance on the steel, so that the P is less than or equal to 0.025 and the S is less than or equal to 0.020.
Cr can improve the strength, hardness and atmospheric corrosion resistance of steel, and has obvious effect when other alloy elements are added. Chromium slows down the decomposition speed of austenite, remarkably improves the hardenability of steel, has a secondary hardening effect, and increases the temper brittleness tendency of steel. However, if the chromium content is too high, the toughness of the base material and the heat affected zone may be deteriorated, and the Cr element content of the steel of the present invention is designed to be 0.56 to 0.60%.
V and C, O, N both have strong binding capacity and form extremely stable compounds with the V and C, O, N, so that crystal grains can be refined, the heat sensitivity and the temper brittleness of the steel are reduced, and the content of the V element in the steel is designed to be 0.13-0.15%.
Ti has low solid solubility in steel, is easy to precipitate in austenite, is pinned at a crystal boundary, prevents grains from growing and recrystallizing, and can play a role of refining the grains, and is also a strong deoxidizer in steel, so that the internal structure of the steel can be compact, the aging sensitivity and the cold brittleness can be reduced, the welding performance can be improved, and in addition, ti is easy to appear in a form of interphase precipitation in the transformation process from austenite to ferrite due to low solid solubility, and the high-temperature strength can be improved, and the content of Ti in the steel is designed to be 0.09-0.10%.
Nb is dissolved in austenite in a solid solution in the rolling process and is subjected to deformation induction to precipitate niobium carbonitride particles, so that the non-recrystallization temperature of austenite is obviously improved, austenite grains are refined, further, grains of ferrite and the like are refined, and the strength is improved. Nb is dissolved in austenite in a solid solution, hardenability can be improved, and carbonized Nb particles precipitated in the quenching process or a second phase precipitated by compounding with V, mo improve high-temperature strength, so that the Nb content in the steel is designed to be 0.05-0.07%.
Al element plays a role in fixing N to form AlN to generate a pinning effect on the original austenite grain boundary, so that the activation energy of austenite grain growth is improved, the austenite grain growth during heating is prevented, and meanwhile, the austenite recrystallization process during deformation can be inhibited. The Al element content in the steel is designed to be 0.06% -0.07%.
N and alloy elements V, ti and the like are easy to produce nitride or nitrogen carbide, so that crystal grains are refined, and the strength and toughness of the steel are improved through precipitation strengthening; on the other hand, if the mass percentage of N in the steel is too high, void defects are easily generated, and the content of the N element in the steel is designed to be 0.0170-0.0200%.
RE is known to be clean and significantly deteriorated in steel. The cleanliness of steel is continuously improved, and the microalloying effect of rare earth elements is increasingly prominent. The microalloying of the rare earth comprises solid solution strengthening of trace rare earth elements, interaction of the rare earth elements with other solute elements and compounds, the existing state (atoms, inclusions or compounds), size, form and distribution of the rare earth elements, particularly segregation at grain boundaries and influence of the rare earth on the steel surface and matrix structure, and the content of the RE element in the steel is designed to be 0.0010-0.0020 percent.
Compared with the prior art, the invention has the beneficial technical effects that:
the invention provides the 1100 MPa-tensile-strength non-quenched and tempered steel which is simple in chemical components, and has the advantages of simplicity in control, low manufacturing cost, strong operability and the like aiming at the production of 1100 MPa-grade non-quenched and tempered steel.
Detailed Description
The present invention is further illustrated by the following specific examples, which are provided for illustrative purposes only and are not to be construed as limiting the scope of the present invention.
The invention is further described below:
table 1 is a table listing the chemical components and weight percent content of each example of the invention;
table 2 is a table of the results of mechanical and toughness tests of the examples of the present invention.
TABLE 1
| Examples | C | Si | Mn | P | S | N | V | Cr | RE | Ti | Nb | Al |
| 1 | 0.28 | 0.94 | 1.81 | 0.019 | 0.09 | 0.0170 | 0.14 | 0.56 | 0.0012 | 0.10 | 0.06 | 0.06 |
| 2 | 0.29 | 0.95 | 1.83 | 0.019 | 0.08 | 0.0175 | 0.15 | 0.56 | 0.0015 | 0.09 | 0.05 | 0.07 |
| 3 | 0.28 | 0.95 | 1.82 | 0.020 | 0.09 | 0.0180 | 0.14 | 0.58 | 0.0015 | 0.10 | 0.05 | 0.06 |
TABLE 2
As can be seen from tables 1 and 2, the VN alloy and the microalloy elements such as Ti, nb and Al are compositely reinforced, so that the technical requirement of the non-quenched and tempered steel with the tensile strength of 1100MPa can be met.
The 1100 MPa-tensile-strength non-quenched and tempered steel has simple chemical components, and has the advantages of simple control, low manufacturing cost, strong operability and the like aiming at the production of 1100 MPa-grade non-quenched and tempered steel.
The above-described embodiments are only intended to illustrate the preferred embodiments of the present invention, and not to limit the scope of the present invention, and various modifications and improvements made to the technical solution of the present invention by those skilled in the art without departing from the spirit of the present invention should fall within the protection scope defined by the claims of the present invention.
Claims (4)
1. A production and preparation method of non-quenched and tempered steel with tensile strength of 1100MPa is characterized in that a steel-making process comprises the following steps: converter-external refining-VD vacuum treatment-continuous casting blank, performing Ar blowing operation in the whole process, performing desulfurization according to the components and temperature of molten steel in the converter, performing component fine adjustment and heating operation, wherein the deep vacuum time is more than or equal to 13min, ensuring that the soft blowing time is more than 18min, preventing the molten steel from being exposed during soft blowing, and performing constant-pulling-speed operation at the superheat degree of less than or equal to 30 ℃;
the steel rolling process flow comprises the following steps: heating a casting blank, removing phosphorus by high-pressure water, cogging in a phi 850mm cogging mill, rolling in a phi 700mm multiplied by 3+ phi 550mm multiplied by 4 continuous rolling mill, sawing, slow cooling, nondestructive testing, stacking, checking, grinding, bundling, warehousing and delivering; the technical parameters controlled in the rolling process are as follows:
heating at 1150-1200 deg.c for 3 hr;
the initial rolling temperature is less than or equal to 1050 ℃;
the finishing temperature is less than or equal to 870 ℃;
the slow cooling temperature is more than or equal to 450 ℃;
the slow cooling time is more than or equal to 48 hours;
the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28% -0.30%, si: 0.94-1.23%, mn: 1.80-1.86%, P is less than or equal to 0.025%, S is 0.08-0.09%, V: 0.13-0.15%, cr: 0.56-0.60%, ti:0.09% -0.10%, al:0.06 percent to 0.07 percent; nb:0.05 percent to 0.07 percent; RE: 0.0010-0.0020%, N: 0.0170-0.0200% of Fe and other trace impurity elements in balance;
the tensile strength of the prepared non-quenched and tempered steel is 1150-1200MPa.
2. The production method of the non-quenched and tempered steel with the tensile strength of 1100MPa according to claim 1, wherein the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28%, si:0.94%, mn:1.81%, P:0.019%, S:0.09%, V:0.14%, cr:0.56%, ti:0.10%, al:0.06 percent; nb:0.06 percent; RE:0.0012%, N:0.0170 percent, and the balance of Fe and other trace impurity elements.
3. The production method of the non-quenched and tempered steel with the tensile strength of 1100MPa according to claim 1, wherein the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.29%, si:0.95%, mn:1.83%, P:0.019%, S:0.08%, V:0.15%, cr:0.56%, ti:0.09%, al:0.07 percent; nb:0.05 percent; RE:0.0015%, N:0.0175 percent, and the balance of Fe and other trace impurity elements.
4. The production method of the non-quenched and tempered steel with the tensile strength of 1100MPa according to claim 1, wherein the non-quenched and tempered steel comprises the following chemical components in percentage by mass: c:0.28%, si:0.95%, mn:1.82%, P:0.020%, S:0.09%, V:0.14%, cr:0.58%, ti:0.10%, al:0.06 percent; nb:0.05 percent; RE:0.0015%, N:0.0180 percent, and the balance of Fe and other trace impurity elements.
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| CN115896592A (en) * | 2022-11-01 | 2023-04-04 | 包头钢铁（集团）有限责任公司 | Preparation method of 25MnCrNiMoA hot-rolled round steel for train hook enclosure frame |
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| CN112342462B (en) * | 2020-10-12 | 2022-02-01 | 马鞍山钢铁股份有限公司 | Nb-Ti microalloyed high-strength high-toughness bainite non-quenched and tempered steel for high-power engine crankshaft and preparation method thereof |
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