CN108220806A - Ultra-high-strength/tenacity abrasion-resistant stee and its manufacturing method - Google Patents
Ultra-high-strength/tenacity abrasion-resistant stee and its manufacturing method Download PDFInfo
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- CN108220806A CN108220806A CN201810036223.1A CN201810036223A CN108220806A CN 108220806 A CN108220806 A CN 108220806A CN 201810036223 A CN201810036223 A CN 201810036223A CN 108220806 A CN108220806 A CN 108220806A
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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
- C22C38/34—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of silicon
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
-
- 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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
-
- 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
- C21D6/002—Heat treatment of ferrous alloys containing Cr
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium 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
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium 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
- C21D2211/002—Bainite
-
- 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
- C21D2211/008—Martensite
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
- Forging (AREA)
Abstract
The invention discloses a kind of ultra-high-strength/tenacity abrasion-resistant stee and preparation method thereof, the chemical composition of steel is wt%:C 0.25~0.55, Si 1.50~2.50, Mn 1.50~2.20, Cr 0.3~1.0, Mo 0.2~0.8, Re 0.01~0.1, S ＜ 0.01, P ＜ 0.01, remaining is Fe.Steel scrap or molten iron are equipped with alloy material through electric arc furnaces or intermediate frequency furnace melting, then through VOD, LF refining, are shaped using continuous casting or molding.Continuous casting billet or ingot rolling or forging and molding, then after special thermal treatment, part 1800~2000MPa of tensile strength, elongation percentage 16~18%, 60~80J/cm of impact flexibility aku2, hardness HRC 55~62.This superpower wear-resistant steel not only has welding performance, but also is a kind of 2000MPa grades of super-high strength steels that elongation after fracture can reach 18% with prominent plasticity.
Description
Technical field
The present invention relates to carbon and low-alloy ultra-high-strength/tenacity abrasion-resistant stee in 1800~2000MPa grades of SiMnCrMoRe systems of one kind,
More particularly to a kind of ultra-high-strength/tenacity abrasion-resistant stee and its manufacturing method.
Background technology
Metallurgical coal mine field is huge to the demand of wear-resistant material.Compared with wear resistant cast iron, abrasion-resistant stee has both because of it
The comprehensive performance of hardness, intensity and toughness is the wear-resistant material being most widely used.In the developing history of abrasion-resistant stee,
Show that specific conclusion, bainitic steel, austenite/bainite dual-phase steel, martensite/bainite dual-phase steel etc. is all shown most
For excellent comprehensive performance.In recent years, using silicon as main alloy element, using silicon during bainite transformation strong inhibition
The characteristics of Carbide Precipitation, can be obtained by carbide-free Bainite ferrite and the residual austenite stabilized by carbon, silicon
Ao-shellfish duplex structure of body composition, since carbides-free eliminates crackle or peels off inducement, thus with excellent obdurability
Comprehensive mechanical property is the high-strength and high ductility abrasion-resistant stee of new generation favored the most in the world at present, still, in a little higher than steel horse
Family name's body transition temperature carry out for a long time (1~3 week) overcooling austenite low temperature bainite isothermal transformation, although obtain by
The nanostructured carbide-free Bainite group of the lath bainitic ferrite of 30 100 nanometer grade thickness and retained austenite composition
It knits, and with superhigh intensity and higher fracture toughness and preferable compression plasticity, but its isothermal transformation speed is extremely slow
Slowly.Because the industrial period is long, efficiency is low, and its phosphorus content is more than 0.6%, belongs to high-carbon alloy steel, welding performance
Difference hardly results in application.Although in subsequent research, add in Co and Al and accelerate bainite transformation speed, reducing Mn ratios increases
Co can more effectively accelerate bainite transformation, and bring significant cost reduction, but in large-scale production, particularly greatly
The isothermal quenching technique of type workpiece, is difficult to realize in the industrial production.
It is one of target that material researcher is pursued that steel material obdurability improves simultaneously, and thinning microstructure is almost
Unique channel.The low temperature bainite of outstanding performance is exactly obdurability to be enable to improve simultaneously due to tens nanometers of its lath thickness.
How to accelerate bainite-martensite rate of transformation, and ensure that it is high to obtain nanoscale carbide-free Bainite-martensitic structure
Can strong ductile steel realize the key that commercial Application is promoted.Other than appropriately designing the chemical composition of steel, make it have good
Good welding performance, low MS transition temperatures are ensured that it obtains low temperature bainite transformation condition, also to be formed using phase transition
More boundary defects, more bainite nucleation sites are provided, accelerate retained austenite Isothermal Bainite transformation speed
Degree improves industrial production efficiency.
Invention content
There is solderability, malleability, it can be achieved that the low cost of industrialized production surpasses the purpose of the present invention is to provide a kind of
High-strength and high ductility abrasion-resistant stee and its manufacturing method.In order to the embodiment to disclosure some aspects there are one basic understanding, below
Give simple summary.The summarized section is not extensive overview, nor to determine key/critical component or description
The protection domain of these embodiments.Its sole purpose is that some concepts are presented with simple form, detailed in this, as below
The preamble of explanation.
The present invention is achieved through the following technical solutions：
A kind of ultra-high-strength/tenacity abrasion-resistant stee, the chemical composition of steel is wt%:C 0.25~0.45%, Si
1.50~2.20%, Mn 1.50~2.20%, Cr 0.30~1.0%, Mo 0.20~1.0%, Re 0.01~
0.1%, S ＜ 0.01%, P ＜ 0.01%, remaining is Fe.
A kind of preparation method of ultra-high-strength/tenacity abrasion-resistant stee, including：
(1) electric arc furnaces or intermediate frequency furnace are smelted, LF, VOD refining, 1550 ± 20 DEG C of tapping temperature, pour into ingot mould or
Continuous cast mold；
(2) steel ingot or continuous casting billet become section bar or forging after rolling or forging and molding, are heated to 930 ± 20 DEG C, heat preservation
After 1.5~3h furnace cooling to less than 400 DEG C when come out of the stove, made annealing treatment；
(3) machined part or forging are heated to 940 ± 20 DEG C, and heat preservation quenches after 20min to 3 hours；
(4) quenched high-strength wearable steel is tempered, 150 DEG C~450 DEG C, tempering time 2h~10h of temperature,
It is air-cooled after tempering, ultra-high-strength/tenacity abrasion-resistant stee is prepared, microscopic structure is carbide-free Bainite-martensite heterogeneous structure,
Lath thickness be 10~50nm, tensile strength sigmab1800~2000MPa, yield strength σs1300~1520MPa, elongation percentage δ 16
~18%, the contraction percentage of areaImpact flexibility aku60~80J/cm2, hardness HRC55~62.
Compared with prior art, the present invention including following advantageous effect：
In the prior art, high-carbon (%C0.7~0.9) low temperature bainite high-strength steel, welding performance is very poor, and is easily formed
Brittlement phase cementite, there are the danger of potential brittleness.The defects of of the invention customer service completely prior art.Through heat treatment after forging, obtain
10~30nm lath thickness carbide-free Bainite-martensite line and staff control, there is the strength and ductility product of 33GPa%, tension is strong
1800~2000MPa of degree, elongation after fracture 16.5~18%, the contraction percentage of area 38~42/%, impact flexibility aku 60~
80J/cm2, hardness HRC 55~62；When particularly intensity is 2000MPa, elongation after fracture remains to reach 18%.
In the present invention, the solderability of steel and malleable functional has prominent plasticity, significant elongation percentage, the impact tough
Property and hardness, make its application field extensive；Meanwhile Q-tempering technique overcomes that the isothermal transformation process time is long, and efficiency is low
Drawback.
It should be understood that above general description and following detailed description are only exemplary and explanatory, not
It can the limitation present invention.
Description of the drawings
Attached drawing herein is incorporated into specification and forms the part of this specification, shows the reality for meeting the present invention
Example is applied, and is used to explain the principle of the present invention together with specification.
Fig. 1 is bainite-martensite lath structure structure chart in the present invention；
Fig. 2 illustrates for heat treatment process in the present invention；
Specific embodiment
It is described below and specific embodiments of the present invention is fully shown, to enable those skilled in the art to put into practice
They.
As shown in Figure 1, for bainite-martensite lath structure structure chart in the present invention；As shown in Fig. 2, in the present invention
Heat treatment process is illustrated.
The present invention the mild continuous transition curve such as determines, it is determined that hot after forging on the basis of the composition design to steel
Treatment process.After quenched, tempering heat treatment process, martensite, bainite and retained austenite are analyzed with EBSD technologies
Volume fraction.The lath thickness of bainite, martensite and austenite is determined using high-resolution-ration transmission electric-lens.And determine heat
The tensile property of sample, impact flexibility and hardness number, finally determine heat treatment process after processing, and the technique is suitable for industrialization
Production, overcomes inoperable property of the isothermal quenching technique in industrialized production.
High-strength and high ductility abrasion-resistant stee can be used for " novel high-performance boring machine cutter steel ", and (tension is strong
Degree>2000MPa, heat treatment hardness>56HRC, impact flexibility Aku>20J), high-strength bolt or the third generation can also be made
Automobile high-strength steel (20~40GPa% of strength and ductility product), realizes the lightweight and safety of automobile, can also forge high-strength endless-track plate,
Realize armoring lightweight.
Embodiment 1
It is using drill steel technique produced by the invention：Chemical composition is wt%:C 0.35%, Si 1.50%, Mn
1.50%, Cr0.80%, Mo 0.20%, Re0.01%, S ＜ 0.01%, P ＜ 0.01%, remaining is Fe；Its manufacturing process
For：Intermediate frequency furnace is smelted, LF refining；1550 DEG C of tapping temperature, pour into ingot mould after refining；After steel ingot decaptitating forging and molding
Annealing, machining；Heat parts after keeping the temperature 3h, are quenched to 930 DEG C in 20-40 DEG C of quenching liquid；It is reheated to after quenching
320 DEG C, keep the temperature 5h after it is air-cooled.After this heat treatment, carbide-free Bainite-martensite that lath thickness is 14nm can be obtained
Line and staff control, tensile strength 1950MPa, elongation after fracture 18%, impact flexibility 87.5J/cm2, hardness HRC55.
Embodiment 2
It is using advanced development machine knife bar technique produced by the invention：Chemical composition is wt%:C 0.45%, Si
2.1%, Mn 1.95%, Cr 0.40%, Mo 0.20%, Re 0.02%, S ＜ 0.01%, P ＜ 0.01%, remaining is Fe；
Its manufacturing process is：Intermediate frequency furnace is smelted, LF refining；1560 DEG C of tapping temperature, pour into ingot mould after refining；Steel ingot forges
Into bar, die forging is into knife bar；To 920 DEG C, heat preservation quenches high-frequency induction heating after 3 minutes；350 DEG C are then heated to, keeps the temperature 3h
It is air-cooled afterwards.After this heat treatment, carbide-free Bainite-martensite line and staff control that lath thickness is 20nm, tension can be obtained
Intensity 1960MPa, impact flexibility 60J/cm2, elongation after fracture 16.5%, hardness HRC61.
Embodiment 3
Technique using armoring creeper tread produced by the invention is：Chemical composition is wt%:C 0.40%, Si
1.88%, Mn1.50%, Cr 0.40%, Mo 0.40%, Re 0.02%, S ＜ 0.01%, P ＜ 0.01%, remaining is Fe；
Its manufacturing process is：Intermediate frequency furnace is smelted, LF refining；1560 DEG C of tapping temperature, pour into ingot mould after refining；Steel ingot forges
Into bar, die forging is into armoring creeper tread, 1200 DEG C of initial forging temperature, 920 DEG C of final forging temperature, direct quenching；400 DEG C are heated to, is protected
It is air-cooled after warm 3h.After this heat treatment, carbide-free Bainite-martensite line and staff control that lath thickness is 30nm can be obtained,
Tensile strength 1880MPa, impact flexibility 68J/cm2, elongation after fracture 17%, hardness HRC56.
It should be understood that the invention is not limited in the flow and structure that are described above and are shown in the drawings,
And various modifications and changes may be made without departing from the scope thereof.The scope of the present invention is only limited by appended claim
System.
Claims (2)
1. a kind of ultra-high-strength/tenacity abrasion-resistant stee, which is characterized in that the chemical composition of steel is wt%:C0.25~0.45%, Si
1.50~2.20%, Mn 1.50~2.20%, Cr 0.30~1.0%, Mo 0.20~1.0%, Re 0.01~0.1%, S ＜
0.01%, P ＜ 0.01%, remaining is Fe.
2. a kind of preparation method of ultra-high-strength/tenacity abrasion-resistant stee, including：
(1) electric arc furnaces or intermediate frequency furnace are smelted, and LF, VOD refining, 1550 ± 20 DEG C of tapping temperature pour into ingot mould or continuous casting
Crystallizer；
(2) steel ingot or continuous casting billet become section bar or forging after rolling or forging and molding, are heated to 930 ± 20 DEG C, and heat preservation 1.5~
After 3h furnace cooling to less than 400 DEG C when come out of the stove, made annealing treatment；
(3) machined part or forging are heated to 940 ± 20 DEG C, and heat preservation quenches after 20min to 3 hours；
(4) quenched high-strength wearable steel is tempered, 150 DEG C~450 DEG C of temperature, tempering time 2h~10h, after tempering
It is air-cooled, ultra-high-strength/tenacity abrasion-resistant stee is prepared, microscopic structure is carbide-free Bainite-martensite heterogeneous structure, and lath is thick
It spends for 10~50nm, tensile strength sigmab1800~2000MPa, yield strength σs1300~1520MPa, elongation percentage δ 16~18%,
The contraction percentage of areaImpact flexibility aku60~80J/cm2, hardness HRC55~62.
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| Application Number | Priority Date | Filing Date | Title |
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| CN201810036223.1A CN108220806B (en) | 2018-01-15 | 2018-01-15 | Ultrahigh-strength high-toughness wear-resistant steel and manufacturing method thereof |
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Cited By (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108977631A (en) * | 2018-08-17 | 2018-12-11 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | A kind of high-performance pick and its manufacturing method |
| CN109750231A (en) * | 2019-03-26 | 2019-05-14 | 湖南力神新材料科技有限公司 | A kind of steel alloy and the preparation method and application thereof |
| CN112458261A (en) * | 2020-11-24 | 2021-03-09 | 高博扬 | Preparation method of high-strength steel and high-strength steel |
| CN112522610A (en) * | 2020-11-18 | 2021-03-19 | 北京交通大学 | V-Ti composite bainite non-quenched and tempered steel structure and manufacturing method thereof |
| CN112662957A (en) * | 2020-12-09 | 2021-04-16 | 暨南大学 | Bainite wear-resistant cast steel with strong wear hardening capacity and preparation method and application thereof |
| CN112813362A (en) * | 2020-12-14 | 2021-05-18 | 内蒙古科技大学 | Manufacturing method of high-strength steel and high-strength steel track shoe |
| CN115011867A (en) * | 2022-04-19 | 2022-09-06 | 清华大学 | High-strength-toughness wear-resistant steel lining plate and preparation method thereof |
| CN116265594A (en) * | 2021-12-17 | 2023-06-20 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | High-strength steel for high-performance cutting pick and heat treatment process thereof |
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| CN103255341A (en) * | 2013-05-17 | 2013-08-21 | 宝山钢铁股份有限公司 | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof |
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| CN1477226A (en) * | 2003-08-01 | 2004-02-25 | 清华大学 | Medium-low carbon manganese system self-hardening bainite steel |
| CN103255341A (en) * | 2013-05-17 | 2013-08-21 | 宝山钢铁股份有限公司 | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof |
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Cited By (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108977631A (en) * | 2018-08-17 | 2018-12-11 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | A kind of high-performance pick and its manufacturing method |
| CN109750231A (en) * | 2019-03-26 | 2019-05-14 | 湖南力神新材料科技有限公司 | A kind of steel alloy and the preparation method and application thereof |
| CN112522610A (en) * | 2020-11-18 | 2021-03-19 | 北京交通大学 | V-Ti composite bainite non-quenched and tempered steel structure and manufacturing method thereof |
| CN112458261A (en) * | 2020-11-24 | 2021-03-09 | 高博扬 | Preparation method of high-strength steel and high-strength steel |
| CN112662957A (en) * | 2020-12-09 | 2021-04-16 | 暨南大学 | Bainite wear-resistant cast steel with strong wear hardening capacity and preparation method and application thereof |
| CN112662957B (en) * | 2020-12-09 | 2021-09-17 | 暨南大学 | Bainite wear-resistant cast steel with strong wear hardening capacity and preparation method and application thereof |
| CN112813362A (en) * | 2020-12-14 | 2021-05-18 | 内蒙古科技大学 | Manufacturing method of high-strength steel and high-strength steel track shoe |
| CN116265594A (en) * | 2021-12-17 | 2023-06-20 | 鄂尔多斯市神东天隆矿山机械有限责任公司 | High-strength steel for high-performance cutting pick and heat treatment process thereof |
| CN115011867A (en) * | 2022-04-19 | 2022-09-06 | 清华大学 | High-strength-toughness wear-resistant steel lining plate and preparation method thereof |
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| Publication number | Publication date |
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| CN108220806B (en) | 2022-02-25 |
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