CN113881894B - Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate - Google Patents
Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate Download PDFInfo
- Publication number
- CN113881894B CN113881894B CN202111076281.5A CN202111076281A CN113881894B CN 113881894 B CN113881894 B CN 113881894B CN 202111076281 A CN202111076281 A CN 202111076281A CN 113881894 B CN113881894 B CN 113881894B
- Authority
- CN
- China
- Prior art keywords
- bainite
- lining plate
- wear
- complex phase
- steel
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Active
Links
Images
Classifications
-
- 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
- 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
- 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
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
-
- 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 preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate, and belongs to the technical field of wear-resistant steel and heat treatment thereof. The bainite-martensite complex phase wear-resistant lining plate comprises the following raw material chemical components in percentage by mass: c: 0.3-0.4%, Si: 0.3-0.5%, Mn: 0.5-0.8%, Cr: 1.0 to 1.1%, Ti: 0.4-0.6%, Mo: 0.3-0.4%, Ni: 0.5-0.6%, P<0.03％，S<0.03%, and the balance of Fe and inevitable impurities. According to the method, a large amount of micron-sized precipitates are precipitated from the complex phase steel by adding carbide forming elements and regulating and controlling the heat treatment process, so that the wear resistance of the material is improved on the basis of not increasing the carbon content; in addition, the staged heating and quenching process effectively avoids the problem of cracking of the lining plate in the heat treatment process; the complex phase steel lining plate treated by the method has the hardness of HBW 426-445 and the impact toughness of 25-35J/cm 2 Compared with the carbide-free bainite-martensite complex phase wear-resistant lining plate, the wear resistance is improved by more than 50 percent.
Description
Technical Field
The invention relates to a preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate, belonging to the technical field of high-strength wear-resistant steel and heat treatment thereof.
Background
Impact abrasive wear is a common type of material failure in the mining and ore processing industries. According to incomplete statistics, the consumption of only wear-resistant steel materials reaches about 400 million tons every year in China, and the consumption caused by impact wear accounts for more than 50% of the total consumption. The direct economic loss can reach more than 200 million yuan, and the production safety accidents caused by abrasion failure frequently occur. Therefore, the development of high-performance wear-resistant steel has become a focus of research in the world steel material field.
The Chinese invention patent CN 106282777A discloses a preparation method of a bainite-martensite complex phase wear-resistant steel material, which comprises the following chemical element components in percentage by mass: c: 0.5-0.6%, Si: 2.0-2.2%, Mn: 2.5-2.8%, P < 0.03%, S < 0.03%, and the balance of Fe. The matrix with holes and the inlay are obtained by adopting the regulation and control of heat treatment processes such as smelting, annealing and the like, and then the bainite-martensite complex phase steel is obtained by inlaying the matrix with holes and the inlay. The prepared wear-resistant lining plate has higher strength and hardness, and the service life of the lining plate is greatly prolonged compared with a high manganese steel lining plate. But the production process is complex, the combination of the porous matrix and the inlay is easy to have defects, and the porous matrix and the inlay are difficult to popularize in practical engineering application. At present, most high-strength wear-resistant steels generally have martensite and bainite structures as matrixes, and the hardness of the materials is improved by increasing the carbon content in the industrial production process, so that the wear resistance is improved. However, the increase in carbon equivalent causes a great deal of deterioration in weldability and workability of the material. The second-phase strengthening is a strengthening mode with the smallest brittleness vector except for fine-grain strengthening, and the hard second-phase particles can effectively resist the phenomena of abrasive embedding and deep cutting of the lining plate in impact abrasive wear, so that the wear resistance of the lining plate is greatly improved. Furthermore, for large wear parts such as liners, rapid heating and cooling during heat treatment can result in a large volume change with the problem of direct cracking of the liner.
Therefore, aiming at the defects of the existing high-strength wear-resistant lining plate preparation process, the invention adopts the processes of stepped heating and stepped isothermal quenching by improving the alloy components and the heat treatment process and simultaneously separates out a large amount of micron-sized carbide precipitates to improve the hardness and the wear resistance of the bainite-martensite complex phase steel, so that the wear-resistant lining plate is suitable for being used in an impact abrasive wear environment.
Disclosure of Invention
The invention aims to provide a preparation method of a precipitate-enhanced bainite-martensite complex phase wear-resistant lining plate, which is characterized in that a large amount of micron-sized precipitates are precipitated from bainite-martensite complex phase steel and are synergistically strengthened with a matrix by adding carbide forming elements and carrying out graded regulation and control on a heat treatment process, so that the wear resistance of the material under the working condition of impact abrasive wear is improved, and the cracking of the lining plate under the heat treatment condition is avoided, and the preparation method specifically comprises the following steps:
(1) smelting and pouring: comprises the following chemical element components in percentage by mass: c: 0.3-0.4%, Si: 0.3-0.5%, Mn: 0.5-0.8%, Cr: 1.0-1.1%, Ti: 0.4-0.6%, Mo: 0.3-0.4%, Ni: 0.5-0.6 percent of raw materials, less than 0.03 percent of P, less than 0.03 percent of S and the balance of Fe and inevitable impurities, and then smelting and pouring to obtain an as-cast steel ingot; high strength steels generally improve wear resistance by increasing C content to increase hardness, but this reduces weldability of the material, and in order to improve both wear resistance and workability of the material, wear resistance is improved by adding alloying elements to form precipitates.
(2) The heat treatment quenching process comprises the following steps: putting the cast steel ingot into a heating furnace, heating to 500 +/-20 ℃ at a speed of 65-80 ℃/h, preserving heat for 20-30min, then heating to 900 +/-20 ℃ at a speed of 65-80 ℃/h, carrying out austenitizing, preserving heat for 1.5-3 h, putting a sample into a quenching bath, monitoring the surface temperature of a steel billet, taking out the steel billet when the temperature of the steel billet is reduced to 600 +/-50 ℃, carrying out air cooling for 30-40min, then carrying out water quenching again, taking out the steel billet when the temperature is reduced to 300 +/-50 ℃, putting the steel billet into a salt bath, keeping the temperature of the steel billet unchanged, carrying out isothermal treatment to obtain bainite, and preserving heat for 1.5h according to the effective thickness of every 50 mm; and then air-cooling to room temperature, and finally performing stress relief tempering to obtain the precipitate reinforced bainite-martensite complex phase wear-resistant steel.
Preferably, the smelting process in step (1) of the invention is as follows: putting an iron block into a crucible, heating to 1450 +/-50 ℃, adding a ferrosilicon block, a ferromanganese block and a ferrochromium block into the furnace, continuously heating to fully melt the ferrosilicon block, the ferromanganese block and the ferrochromium block, keeping the temperature when the temperature is heated to 1500 plus or minus 1550 ℃, continuously adding a titanium ingot, a molybdenum wire and a nickel wire into the furnace to perform alloying smelting, continuously smelting for 30-50min, pouring after removing impurities, controlling the pouring process within 3min, drilling steel scraps from different positions after a casting is cooled, and then performing chemical component analysis to control components within an alloying regulation range.
Preferably, the temperature of the stress-relief tempering is 200 +/-20 ℃, and the time is 1.5-2.5 h.
The principle of the invention is as follows: by optimizing alloy components, the CCT curve of the bainite-martensite complex phase steel is shifted to the right, and micron-sized (Ti, Mo) C precipitates are generated in a structure by adding alloy elements such as Ti, Mo and the like; the hardness and the deformation resistance of the matrix are greatly improved through the second phase strengthening gain of the precipitate, so that the aim of improving the abrasion resistance of the impact abrasive of the bainite-martensite complex phase steel lining plate is fulfilled.
The invention selects Ti as the main precipitated element, TiC has the advantages of high hardness and low density compared with VC and NbC, and the price of Ti is generally lower than that of V and Nb, thus being more suitable for being used as the main precipitated element in industrial production. Aiming at the problems that the traditional large-scale lining plate has uneven internal and external temperature and is easy to crack due to thermal stress in the heat treatment process, the heat treatment process of double-stage heating and staged quenching is designed, so that the bainite-martensite complex phase lining plate can be uniformly heated inside and outside as much as possible in the heat treatment process, and more uniform and stable structure and performance are obtained. In addition, a temperature interval for lower bainite transformation is selected on the basis of isothermal temperature, carbon in super-cooled austenite can be fully distributed and stabilized to room temperature through long-time isothermal treatment, the problem of poor plasticity of a traditional high-strength lining plate is solved, a large amount of work hardening can be generated in the impact wear process by the thin-film residual austenite and the strip-shaped lower bainite structure through deformation induced martensite transformation, and the wear resistance of the high-strength steel is greatly improved.
The invention has the advantages of
(1) According to the invention, the content of C is reduced, and Ti and Mo elements are added to combine with a heat treatment process, so that micron-sized (Ti, Mo) C composite precipitated phases are generated on the lining plate; the micron-sized precipitates resist the embedding of broken abrasive particles into a matrix in the process of impacting abrasive wear, so that the deep cutting caused by relative sliding is avoided, and the wear resistance of the bainite-martensite complex phase lining plate is greatly improved.
(2) The invention adopts a graded heating mode to austenitize, and the temperature rise rates inside and outside the large-scale lining plate can be consistent as much as possible through graded heating, so that the internal stress cracking caused by the overlarge temperature gradient inside and outside the casting is avoided; in addition, the first heating in the stage heating process can accumulate enthalpy for the second heating, and provide driving force for subsequent recrystallization.
(3) The CCT curves of ferrite and pearlite of the material are shifted to the right through alloying design, and the ferrite and pearlite transformation curves can be bypassed without a fast cooling speed; two cooling processes are added in the isothermal quenching process, so that the cracking of the lining plate due to quenching stress in the cooling process is avoided; in addition, through isothermal low bainite transformation temperature salt bath, carbon in super-cooled austenite can be fully distributed and stabilized to room temperature, and the problem that the traditional high-strength lining plate is poor in plasticity is avoided.
(4) The invention utilizes alloying design and heat treatment regulation and control to obtain a complex phase structure containing educts, has higher hardness and impact toughness and high wear resistance, and the wear resistance of the lining plate under the same impact abrasive wear condition is improved by 50 percent compared with the traditional carbide-free complex phase lining plate.
Drawings
FIG. 1 is an SEM image of a wear surface of a bainite-martensite complex phase wear-resistant lining plate without precipitates after 4h of impact grinding material wear.
FIG. 2 is a distribution diagram of elements of example 2 of the precipitate enhanced bainite/martensite dual phase wear resistant liner plate of the present invention.
FIG. 3 is a schematic diagram of a heat treatment process of the precipitate enhanced bainite/martensite complex phase wear-resistant lining plate of the invention.
FIG. 4 is a color metallographic morphology and a graph comparing the distribution of precipitates OM for the embodiment 1 of the precipitate enhanced bainite/martensite complex phase wear-resistant lining plate of the present invention.
FIG. 5 is an SEM image of the form and structure of the precipitate-enhanced bainite/martensite complex phase wear-resistant lining plate.
FIG. 6 is an SEM image of the wear surface of a sample of example 1 in the precipitate-enhanced bainite/martensite complex phase wear-resistant lining plate after 4 hours of impact abrasive wear.
Detailed Description
The present invention will be further described with reference to specific embodiments according to the principle of the present invention, but the scope of the present invention is not limited to the contents.
Example 1
A preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate specifically comprises the following steps:
(1) alloying design: the wear-resistant bainite steel comprises the following chemical element components in percentage by mass: c: 0.30%, Si: 0.35%, Mn: 0.60%, Cr: 1.03%, Ti: 0, 0.2%, 0.4%, 0.6%, Mo: 0.38%, Ni: 0.55%, P < 0.03%, S < 0.03%, and the balance Fe and unavoidable impurities.
(2) Smelting and pouring: the method comprises the steps of putting an iron block into a crucible, heating to 1450 ℃, adding a ferrosilicon block, a ferromanganese block and a ferrochromium block into a furnace, continuing to heat to fully melt the ferrosilicon block, the ferromanganese block and the ferrochromium block, keeping the temperature when the temperature is heated to 1550 ℃, continuing to add a titanium ingot, a molybdenum wire and a nickel wire into the furnace for alloying smelting, continuing to smelt for 50min, beginning to pour after impurities are removed, controlling the pouring process within 3min, drilling steel scraps from different positions after a casting is cooled, and then performing chemical component analysis to control components within an alloying regulation range.
(3) The heat treatment quenching process comprises the following steps: putting the cast steel ingot into a heating furnace, heating to 500 ℃ at the speed of 70 ℃/h, preserving heat for 25min, then heating to 900 ℃ at the speed of 75 ℃/h, carrying out austenitizing, preserving heat for 2.5h, putting a sample into a quenching bath, monitoring the surface temperature of the steel billet, taking out the steel billet when the temperature of the steel billet is reduced to 600 ℃, carrying out air cooling for 35min, then carrying out water quenching again, taking out the steel billet when the temperature is reduced to 300 ℃, putting the steel billet into a salt bath, keeping the temperature of the steel billet unchanged, carrying out isothermal treatment to obtain bainite, and preserving heat for 1.5h according to the effective thickness of 50 mm; then air-cooling to room temperature, and finally performing stress relief tempering to obtain the precipitate enhanced bainite-martensite complex phase wear-resistant steel.
TABLE 1 hardness before and after impact abrasion and impact toughness
TABLE 2 loss of abrasion weight after different abrasion times
| 1h | 2h | 3h | 4h | Total wear amount/g | |
| The content of Ti is 0 percent | 0.28 | 0.61 | 0.80 | 0.85 | 2.54 |
| The content of Ti is 0.2 percent | 0.26 | 0.41 | 0.54 | 0.65 | 1.86 |
| The content of Ti is 0.4 percent | 0.24 | 0.26 | 0.37 | 0.35 | 1.22 |
| The content of Ti is 0.6 percent | 0.26 | 0.29 | 0.38 | 0.47 | 1.4 |
The comparison shows that the content of the precipitates in the lining plate structure can be obviously improved by improving the content of Ti, the hardness of the lining plate sample is obviously improved along with the increase of the precipitates, and the impact toughness is slightly reduced. The wear resistance of the lining plate is also obviously improved along with the increase of the content of Ti, and compared with the lining plate without Ti, the wear resistance of the precipitate enhanced bainite-martensite complex phase lining plate is improved by more than 50 percent; FIG. 1 shows SEM images of the impact abrasives of the backing plate without Ti element, and it can be seen that a large amount of abrasives are embedded into the material matrix without precipitate protection, and the abrasive embedding greatly reduces the wear resistance of the backing plate.
Example 2
A preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate specifically comprises the following steps:
(1) alloying design: the wear-resistant bainite steel comprises the following chemical element components in percentage by mass: c: 0.4%, Si: 0.5%, Mn: 0.80%, Cr: 1.0%, Ti: 0.4%, Mo: 0, 0.2%, 0.3%, 0.4%, Ni: 0.5%, P < 0.03%, S < 0.03%, and the balance Fe and unavoidable impurities.
(2) Smelting and pouring: the method comprises the steps of putting an iron block into a crucible, heating to 1450 ℃, adding a ferrosilicon block, a ferromanganese block and a ferrochromium block into a furnace, continuing to heat to fully melt the ferrosilicon block, the ferromanganese block and the ferrochromium block, keeping the temperature when the temperature is heated to 1550 ℃, continuing to add a titanium ingot, a molybdenum wire and a nickel wire into the furnace for alloying smelting, continuing to smelt for 40min, beginning to pour after impurities are removed, controlling the pouring process within 3min, drilling steel scraps from different positions after a casting is cooled, and then performing chemical component analysis to control components within an alloying regulation range.
(3) The heat treatment quenching process comprises the following steps: putting the cast steel ingot into a heating furnace, heating to 520 ℃ at a speed of 70 ℃/h, preserving heat for 20min, then heating to 900 ℃ at a speed of 80 ℃/h, carrying out austenitizing, preserving heat for 1.5h, putting a sample into a quenching bath, monitoring the surface temperature of the steel billet, taking out the steel billet when the temperature of the steel billet is reduced to 650 ℃, carrying out air cooling for 30min, then carrying out water quenching again, taking out the steel billet when the temperature is reduced to 350 ℃, putting the steel billet into a salt bath, keeping the temperature of the steel billet unchanged, carrying out isothermal treatment to obtain bainite, and preserving heat for 1.5h according to the effective thickness of 50 mm; and then air-cooling to room temperature, and finally performing stress relief tempering to obtain the precipitate reinforced bainite-martensite complex phase wear-resistant steel.
TABLE 3 hardness before and after impact abrasion and impact toughness
TABLE 4 abraded weight loss after different abrasion times
| 1h | 2h | 3h | 4h | Total wear amount/g | |
| The content of Mo is 0 percent | 0.45 | 0.62 | 0.74 | 0.81 | 2.62 |
| The content of Mo is 0.2 percent | 0.36 | 0.42 | 0.51 | 0.66 | 1.95 |
| The content of Mo is 0.3 percent | 0.27 | 0.38 | 0.46 | 0.55 | 1.66 |
| The content of Mo is 0.4 percent | 0.25 | 0.30 | 0.41 | 0.52 | 1.48 |
By comparing the performances of samples with different Mo contents, the single Ti element cannot form composite precipitation with the Mo content; the abrasion resistance of the impact abrasive after the Ti and Mo elements are compositely separated out is obviously improved, and the abrasion resistance is improved by 40% compared with that of the impact abrasive without the Mo element; as shown in the EPMA element distribution diagram of FIG. 2, the diagrams a, b, C and d respectively show the substrate morphology, the C element distribution, the Mo element distribution and the Ti element distribution. It can be seen that Ti and Mo elements can form hard (Ti, Mo) C precipitation, and compared with single TiC precipitation, the TiC precipitation has higher hardness and can effectively protect matrix tissues.
Example 3
A preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate specifically comprises the following steps:
(1) alloying design: the wear-resistant bainite steel comprises the following chemical element components in percentage by mass: c: 0.35%, Si: 0.4%, Mn: 0.50%, Cr: 1.0%, Ti: 0.5%, Mo: 0.38%, Ni: 0.6%, P < 0.03%, S < 0.03%, and the balance Fe and unavoidable impurities.
(2) Smelting and pouring: the method comprises the steps of putting an iron block into a crucible, heating to 1450 ℃, adding a ferrosilicon block, a ferromanganese block and a ferrochromium block into a furnace, continuing to heat to fully melt the ferrosilicon block, the ferromanganese block and the ferrochromium block, keeping the temperature when the temperature is heated to 1550 ℃, continuing to add a titanium ingot, a molybdenum wire and a nickel wire into the furnace for alloying smelting, continuing to smelt for 30min, beginning to pour after impurities are removed, controlling the pouring process within 3min, drilling steel scraps from different positions after a casting is cooled, and then performing chemical component analysis to control components within an alloying regulation range.
(3) The heat treatment quenching process comprises the following steps: putting the cast steel ingot into a heating furnace, heating to 500 +/-20 ℃ at the speed of 70 ℃/h, preserving heat for 20-30min, then heating to 900 +/-20 ℃ at the speed of 65-80 ℃/h, carrying out austenitizing, preserving heat for 1.5-3 h, putting a sample into a quenching bath, monitoring the surface temperature of a steel billet, taking out the steel billet when the temperature of the steel billet is reduced to 600 +/-50 ℃, carrying out air cooling for 30-40min, then carrying out water quenching again, taking out the steel billet when the temperature is reduced to 300 +/-50 ℃, putting the steel billet into a salt bath, keeping the temperature of the steel billet unchanged, carrying out isothermal treatment to obtain bainite, and preserving heat for 1.5h according to the effective thickness of every 50 mm; then air-cooling to room temperature, and finally performing stress relief tempering to obtain the precipitate enhanced bainite-martensite complex phase wear-resistant steel.
Specific conditions are shown in tables 5 and 6:
TABLE 5 hardness before and after impact abrasion and impact toughness
TABLE 6 loss of abrasion weight after different abrasion times
Through comparison, the impact toughness of a sample which is not subjected to staged heating and double-stage quenching can be greatly reduced, and very large internal stress can be generated by rapid heating and cooling, so that the large casting such as a lining plate can easily have defects such as cracks and the like. And the hardness and the impact toughness of the sample subjected to graded heating and double-stage quenching are greatly improved.
And (3) comparative analysis:
through the alloying design and the regulation and control of the heat treatment process, the precipitate enhanced bainite-martensite complex phase wear-resistant lining plate with different Ti and Mo contents is respectively prepared, and the performance of the precipitate enhanced bainite-martensite complex phase wear-resistant lining plate is compared with that of a bainite-martensite complex phase wear-resistant lining plate without Ti and Mo elements. It can be found from the metallographic structure of the matrix in fig. 4 that a large amount of (Ti, Mo) C carbide precipitates are dispersed and distributed in the matrix structure of the lining plate after alloying regulation and heat treatment according to the present invention, and the content of the precipitates is further increased and the distribution is more uniform as the content of Ti and Mo is increased. The hard precipitate particles have extremely high hardness, and can effectively protect the matrix during the abrasion process of the impact abrasive, and prevent matrix tissues from being embedded by abrasive fragments. In addition, as can be seen from the enlarged structure of fig. 5, after the heat treatment regulation, a large amount of film-shaped retained austenite exists in the matrix, and the film-shaped retained austenite can effectively improve the ductility and toughness of the material, so that the lining plate has higher wear resistance. The CCT curve of the liner plate was shifted to the right by alloying treatment and although isothermal at 600 c for a period of time, ferrite and pearlite were not observed in the matrix structure, indicating that the selected staged quenching process did not affect the hardness of the matrix while effectively improving the thermal stress cracking of the liner plate. The impact toughness of the material is greatly improved compared to single stage heated and directly quenched liner samples.
Samples of the bainite-martensite complex phase wear-resistant lining plates prepared in the above examples 1 to 3 at different three positions were respectively cut out to carry out an impact grinding abrasion test, the impact work was set to 1J, the granularity of the grinding material was 20 to 40 meshes, and pre-abrasion was carried out for 20min before impact to obtain a suitable abrasion contact surface. After 4h of abrasion of the impact abrasive, the matrix hardness, the hardness after impact and the impact toughness of the sample are shown in tables 1, 3 and 5; the weight loss on impact abrasive wear is shown in tables 2, 4, 6. The carbide-free bainite-martensite wear-resistant steel without Ti and Mo is lowest in wear resistance, and the samples subjected to single-stage heating and single-stage quenching are lowest in impact toughness. Further, as shown in FIG. 6 (panel a is the wear profile of the backing plate without precipitates, panel b is an enlarged view thereof, panel c is the wear profile of the backing plate with precipitates, and panel d is an enlarged view) after impact wear, the backing plate without precipitates being strengthened is accompanied by a large amount of abrasive insertion and deep plowing, which severely reduces the wear resistance of the backing plate. The hardness, impact toughness and wear resistance of the bainite-martensite wear-resistant lining plate are obviously improved through the alloying design and heat treatment regulation.
Claims (3)
1. A preparation method of a precipitate enhanced bainite-martensite complex phase wear-resistant lining plate is characterized by comprising the following steps: by adding carbide forming elements and carrying out graded regulation and control on a heat treatment process, a large amount of micron-sized precipitates are separated out from the bainite-martensite complex phase steel, and the cracking of a lining plate during heat treatment is avoided, and the method specifically comprises the following steps:
(1) smelting and pouring: comprises the following chemical element components in percentage by mass: c: 0.3-0.4%, Si: 0.3-0.5%, Mn: 0.5-0.8%, Cr: 1.0-1.1%, Ti: 0.2-0.6%, Mo: 0.3-0.4%, Ni: 0.5-0.6 percent of raw materials, less than 0.03 percent of P, less than 0.03 percent of S and the balance of Fe and inevitable impurities, and then smelting and pouring to obtain an as-cast steel ingot;
(2) the heat treatment quenching process comprises the following steps: putting the cast steel ingot into a heating furnace, heating to 500 +/-20 ℃ at a speed of 65-80 ℃/h, preserving heat for 20-30min, then heating to 900 +/-20 ℃ at a speed of 65-80 ℃/h, carrying out austenitizing, preserving heat for 1.5-3 h, putting a sample into a quenching bath, monitoring the surface temperature of a steel billet, taking out the steel billet when the temperature of the steel billet is reduced to 600 +/-50 ℃, carrying out air cooling for 30-40min, then carrying out water quenching again, taking out the steel billet when the temperature is reduced to 300 +/-50 ℃, putting the steel billet into a salt bath, keeping the temperature of the steel billet unchanged, carrying out isothermal treatment to obtain bainite, and preserving heat for 1.5h according to the effective thickness of every 50 mm; and then air-cooling to room temperature, and finally performing stress relief tempering to obtain the precipitate reinforced bainite-martensite complex phase wear-resistant steel.
2. The method for preparing the precipitate-enhanced bainite-martensite complex phase wear-resistant lining plate according to claim 1, is characterized in that: the smelting process of the step (1) comprises the following steps: putting an iron block into a crucible, heating to 1450 +/-50 ℃, adding a ferrosilicon block, a ferromanganese block and a ferrochromium block into the furnace, continuously heating to fully melt the ferrosilicon block, the ferromanganese block and the ferrochromium block, keeping the temperature when the temperature is heated to 1500 plus or minus 1550 ℃, continuously adding a titanium ingot, a molybdenum wire and a nickel wire into the furnace to perform alloying smelting, continuously smelting for 30-50min, pouring after removing impurities, controlling the pouring process within 3min, drilling steel scraps from different positions after a casting is cooled, and then performing chemical component analysis to control components within an alloying regulation range.
3. The method for preparing the precipitate-enhanced bainite-martensite complex phase wear-resistant lining plate according to claim 1, is characterized in that: the temperature of the stress relief tempering is 200 +/-20 ℃, and the time is 1.5-2.5 h.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111076281.5A CN113881894B (en) | 2021-09-14 | 2021-09-14 | Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202111076281.5A CN113881894B (en) | 2021-09-14 | 2021-09-14 | Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN113881894A CN113881894A (en) | 2022-01-04 |
| CN113881894B true CN113881894B (en) | 2022-09-09 |
Family
ID=79009104
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202111076281.5A Active CN113881894B (en) | 2021-09-14 | 2021-09-14 | Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN113881894B (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN114369771B (en) * | 2022-01-13 | 2022-11-18 | 鞍钢股份有限公司 | High-toughness wear-resistant steel with excellent cold bending property and manufacturing method thereof |
| CN115679234B (en) * | 2022-11-30 | 2023-06-02 | 昆明理工大学 | Method for improving wear-resistant and corrosion-resistant properties of zirconium-based amorphous alloy |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP3030675B2 (en) * | 1993-04-02 | 2000-04-10 | エヌケーケー条鋼株式会社 | Manufacturing method of wear-resistant steel bar |
| CN103266269B (en) * | 2013-05-15 | 2015-04-22 | 武汉钢铁(集团)公司 | HB500 grade hot continuous rolling high strength wear-resisting steel and production method thereof |
| CN106282777B (en) * | 2016-09-09 | 2018-05-25 | 昆明理工大学 | One kind inlays bainite-martensite Multiphase Steel wear-resistant liner and preparation method thereof |
| CN109680221A (en) * | 2019-01-17 | 2019-04-26 | 山东钢铁股份有限公司 | A kind of high tenacity granules reinforced wear resistance steel and preparation method thereof |
| CN109825774B (en) * | 2019-04-11 | 2020-12-11 | 紫荆浆体管道工程股份公司 | Preparation method of bainite-martensite multiphase wear-resistant corrosion-resistant steel |
| CN111394661B (en) * | 2020-04-30 | 2021-07-27 | 西京学院 | Preparation process of low-alloy high-strength-toughness martensite duplex phase steel |
-
2021
- 2021-09-14 CN CN202111076281.5A patent/CN113881894B/en active Active
Also Published As
| Publication number | Publication date |
|---|---|
| CN113881894A (en) | 2022-01-04 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US20220162731A1 (en) | Hot-working die steel, heat treatment method thereof and hot-working die | |
| CN104388821B (en) | TiC particulate reinforcement type heterogeneous structure high-ductility wear-resisting steel plate and manufacture method | |
| WO2022135268A1 (en) | Carbide-containing high-strength and -toughness bainitic wear-resistant steel and preparation method therefor | |
| CN106978564A (en) | A kind of precipitation hardening type plastic die steel and preparation method thereof | |
| CN113881894B (en) | Preparation method of precipitate-enhanced bainite-martensite complex-phase wear-resistant lining plate | |
| CN107974636A (en) | A kind of high rigidity high-hardenability pre-hardening plastic die steel and preparation method thereof | |
| CN113249645B (en) | High-ductility and ultrahigh-strength ductile steel and preparation method thereof | |
| CN111826589B (en) | Plastic die steel with high strength and high corrosion resistance and preparation method thereof | |
| CN114411043B (en) | Preparation method of large hot forging hot work die steel | |
| CN106756619B (en) | A kind of high-toughness high-strength abrasion-proof steel ball and preparation method thereof | |
| CN108315652B (en) | Inexpensive high-hardenability HB450 grades of cut deal wear-resisting steel plates and manufacturing method | |
| WO2021208181A1 (en) | Low-temperature, high-toughness, high-temperature, high-intensity and high-hardenability hot mold steel and preparation method therefor | |
| CN108149156A (en) | A kind of big specification high uniformity abrasion-resistant stee and its manufacturing method | |
| CN114717488A (en) | 1800MPa grade high-ductility high-corrosion-resistance maraging stainless steel and preparation method thereof | |
| CN113897541B (en) | High-chromium wear-resistant steel ball and casting process thereof | |
| CN113502431A (en) | Isothermal quenching nodular cast iron material and preparation method and application thereof | |
| CN102719766B (en) | Wear-resistant steel with high strength and production method thereof | |
| CN108715976B (en) | Ti-Zr-C particle reinforced wear-resistant steel and preparation method thereof | |
| CN110106451A (en) | Carbon abrasion resistant cast steel and its heat treatment method in a kind of high silicon | |
| CN107779786A (en) | A kind of wear-resistant ball and its preparation technology | |
| CN114517276A (en) | Ultra-low carbon high-performance maraging stainless steel and preparation method thereof | |
| CN114196892A (en) | Nb-V alloyed high manganese steel and preparation method and application thereof | |
| CN109694994B (en) | Corrosion-resistant high-wear-resistant steel ball and manufacturing method thereof | |
| CN110396641A (en) | A kind of good Micro Alloying HB360 grades of cut deal abrasion-resistant stees of harden ability and its production method | |
| CN114457284B (en) | High-silicon stainless steel material containing vanadium and titanium and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |