CN115354217B

CN115354217B - Impact-abrasion-resistant complex-phase structure hammer head and preparation method thereof

Info

Publication number: CN115354217B
Application number: CN202210779145.0A
Authority: CN
Inventors: 高博; 李昭东; 曹燕光; 雍岐龙; 杨忠民; 陈颖; 王慧敏
Original assignee: Zhonglian Advanced Steel Technology Co ltd; Central Iron and Steel Research Institute
Current assignee: Zhonglian Advanced Steel Technology Co ltd; Central Iron and Steel Research Institute
Priority date: 2022-07-04
Filing date: 2022-07-04
Publication date: 2023-03-03
Anticipated expiration: 2042-07-04
Also published as: CN115354217A

Abstract

The invention discloses an anti-impact-abrasion complex-phase structure hammer head and a preparation method thereof, relates to the technical field of abrasion-resistant steel for crushing, and solves the problems that the hammer head in the prior art is too quickly abraded and the preparation cost of the hammer head is high in a crushing operation environment with impact and abrasion functions. The microstructure 10mm below the surface layer of the hammer comprises 15-30% of sheet bainite and 3-8% of residual austenite in percentage by volume, and the balance is martensite; the microstructure at the position of 25mm below the surface layer of the hammer head comprises 5-10% of sheet bainite, 35-50% of lath-shaped bainite and 5-15% of residual austenite in percentage by volume, and the balance is martensite. The preparation method comprises smelting, casting and forming, processing, homogenizing treatment, quenching and tempering. The hammer head can be used for a hammer crusher.

Description

Impact-abrasion-resistant complex-phase structure hammer head and preparation method thereof

Technical Field

The invention relates to the technical field of wear-resistant steel for crushing, in particular to an impact-abrasion-resistant complex-phase structure hammer head and a preparation method thereof.

Background

The hammer crusher is widely applied to crushing operation in the industries of cement, mine, coal, metallurgy and the like. The hammer head is a core working part for crushing materials by the hammer crusher, is subjected to comprehensive actions of impact, abrasion and the like of the materials in the operation process, has complex and severe working conditions, and is required to have the properties of high strength, high toughness, high wear resistance and the like.

The existing hammer head is mainly made of high manganese steel or alloy steel taking medium-low carbon martensite as a matrix. Wherein, the high manganese steel hammer often fails prematurely due to abrasion damage in the service process. The main reasons for its rapid wear include two aspects: on one hand, the high manganese steel has low initial hardness and is easy to wear in the initial service stage; on the other hand, when the impact load is low, the high manganese steel hammer head cannot sufficiently exert the work hardening effect, and is thus easily worn. In order to improve the wear resistance of high manganese steel, people build up a wear-resistant layer on the working end of the high manganese steel, cast high chromium cast iron, hard alloy and the like in an inlaying mode, and therefore prepare the composite hammer head with better wear resistance.

The alloy steel hammer head using the medium-low carbon martensite as the matrix has lower toughness and is easy to crack in a crushing operation environment with impact and abrasion functions. In addition, in terms of the working efficiency of the whole period of the crushing operation, the hammer head is required to have high wear resistance not only in the early stage of use, but also in the later stage of use. In the case of ordinary medium-low carbon alloy steel, insufficient hardenability causes insufficient depth of a hardened layer, resulting in accelerated wear. The addition of alloying elements to achieve high hardenability also increases product costs.

Disclosure of Invention

In view of the above analysis, the invention aims to provide an anti-impact-abrasion complex phase structure hammer head and a preparation method thereof, and solves the problems that the hammer head in the prior art is too quickly abraded in a crushing operation environment with impact and abrasion functions and the preparation cost of the hammer head is high.

The purpose of the invention is mainly realized by the following technical scheme:

the invention provides an anti-impact wear complex phase structure hammer head, wherein a microstructure at a position 10mm below the surface layer of the hammer head comprises 15-30% of sheet bainite and 3-8% of residual austenite according to volume fraction, and the balance is martensite; the microstructure at the position of 25mm below the surface layer of the hammer head comprises 5-10% of sheet bainite, 35-50% of lath-shaped bainite and 5-15% of residual austenite in percentage by volume, and the balance is martensite.

Further, the alloy raw materials of the impact-abrasion-resistant complex-phase structure hammer head comprise the following components in percentage by mass: 0.25 to 0.45wt.% of C, 1.8 to 2.2wt.% of Mn1.3 to 1.7wt.% of Si, 0.6 to 1.0wt.% of Cr0.1 to 0.45wt.% of Mo0.1 to 0.45wt.%, and the balance of Fe and inevitable impurities.

Furthermore, the tensile strength of 10mm is 1620-1740 MPa, the yield strength is 1280-1300 MPa, the Rockwell hardness is 48-50 HRC, and the impact energy is 34-55J; the tensile strength at the position of 25mm is 1510-1580 MPa, the yield strength is 1190-1230 MPa, the Rockwell hardness is 45-46 HRC, and the impact energy is 45-64J.

The invention also provides a preparation method of the impact wear resistant complex phase structure hammer head, which is used for preparing the impact wear resistant complex phase structure hammer head and comprises the following steps:

step 1: smelting, deoxidizing, deslagging and casting the alloy raw material to obtain a cast ingot;

step 2: processing the cast ingot into a hammer head;

and step 3: carrying out homogenization treatment on the hammer head;

and 4, step 4: re-austenitizing the homogenized hammer head, and quenching and cooling to room temperature after discharging;

and 5: and tempering and preserving the heat of the quenched hammer, and air-cooling the hammer to room temperature after discharging to obtain the impact-abrasion-resistant complex phase structure hammer.

Further, in step 3, the homogenization treatment comprises the following steps:

heating the hammer to 1000-1100 deg.c and maintaining for 8-12 hr.

Further, in the step 4, the heating temperature is 880 to 930 ℃.

Further, in the step 4, the heat preservation time is 60-90 min.

Further, in step 4, the cooling comprises the following steps:

rapidly cooling to below 400 ℃ at a cooling rate of 1-30 ℃, and slowly cooling to room temperature at a cooling rate of 0.1-0.5 ℃/s.

Further, in the step 5, the tempering temperature is 250-350 ℃.

Further, in the step 5, the heat preservation time is 2-4 h.

Compared with the prior art, the invention can realize at least one of the following beneficial effects:

a) According to the impact-abrasion-resistant complex phase structure hammer head provided by the invention, the distribution gradient of the microstructure from the surface layer to the core part of the hammer head is changed. Wherein, the cooling speed of the part 10mm below the surface layer of the hammer head is higher, and the hammer head at the part enters a flaky bainite and martensite phase transformation area. The size of the flaky bainite and martensite products at the part is small, and the flaky bainite and martensite products contain a certain amount of residual austenite, so that the matching of the toughness of the hammer head is facilitated, and therefore, the hammer head can show good impact and abrasion resistance in the initial service stage. The cooling speed at the position 25mm below the surface layer of the hammer head is slower, which is different from the tissue type close to the surface layer of the hammer head, the contents of flaky bainite and martensite in the hammer head are reduced, and the hardness is reduced to some extent. Lath-shaped bainite is introduced into the part, and the content of residual austenite is increased. The bainite ferrite in the lath bainite provides higher hardness and wear resistance, and the residual austenite not only improves the toughness of the hammer but also improves the work hardening capacity of the hammer, so that the hammer can still maintain higher impact and wear resistance in the part although the hardness is reduced.

B) In the actual service process, when the impact load is lower, the impact wear resistant complex phase structure hammer head provided by the invention has lower wear weight loss because the hammer head has higher initial hardness and good toughness matching. When the impact load is higher, the dislocation density of bainite ferrite, martensite and the like in the hammer head is increased under the stress condition, the structure is refined, and the hardness of the abrasion surface layer is improved; the retained austenite is transformed into martensite under the action of a large load, and the work hardening performance of the hammer head is further improved. In addition, under the action of impact load, the failure process of the hammer head comprises the stages of plastic deformation, material peeling and the like, the plastic deformation capacity of the steel is improved due to the existence of an austenite phase, and the compressive stress generated in the process of transforming the austenite to the martensite plays a certain role in inhibiting the crack propagation in the material peeling process. Therefore, in a certain impact load range, the complex phase structure hammer has good impact wear resistance, and can bring beneficial effects for improving the production efficiency of crushing operation.

C) The impact wear resistant complex phase structure hammer provided by the invention is mainly based on low-cost alloy elements, and the manufacturing cost of the hammer can be greatly reduced. The preparation method of the impact-abrasion-resistant complex-phase structure hammer head has the characteristics of easiness in production, simple process, energy conservation and environmental friendliness. After the quenching is finished, the tempering process is added, and one of the main purposes of tempering is to make the austenite further carbon-rich. The austenite distributed in the martensite/austenite islands has low carbon-rich degree and poor mechanical stability, is easy to transform at the initial stage of stress and is not beneficial to the hardening effect in a large range. Through tempering and heat preservation, partial carbon atoms in bainitic ferrite or martensite are distributed into austenite, so that the mechanical stability of the residual austenite is improved. The tempering aims to eliminate internal stress caused by high-carbon martensite transformation at 25mm below the surface layer of the hammer head. The temperature of the hammer head for bainite transformation at the part is higher, and lath-shaped bainite and two morphologies of unconverted austenite are formed. The carbon-rich degree of membranous austenite positioned in the bainite lath is higher, and the membranous austenite can be stably kept to room temperature; the bulk austenite between the bainitic laths in different directions is partially martensitic during subsequent cooling to room temperature due to the low degree of carbon enrichment, forming large bulk martensite/austenite islands. Different from low-carbon martensite formed on the surface layer of the hammer head, the martensite/austenite island has high carbon content at the position 25mm below the surface layer of the hammer head, and generates larger phase-change stress in the phase-change process. In addition, the martensite in the martensite/austenite islands has high hardness and poor toughness, and is easy to crack in the impact process. In conclusion, the internal stress of the hammer head is eliminated through tempering treatment, and partial carbon atoms in the high-carbon martensite are diffused into austenite, so that the mechanical stability of the residual austenite is further improved.

Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and drawings.

Drawings

The drawings are only for purposes of illustrating particular embodiments and are not to be construed as limiting the invention, wherein like reference numerals are used to designate like parts throughout.

FIG. 1 shows the structure morphology of the SEM tissue at a position 10mm below the surface layer of the hammer head in example 1.

FIG. 2 is the structural morphology of the scanning electron microscope at a position 25mm below the surface layer of the hammer head in example 1.

FIG. 3 is the structural morphology of the retained austenite in the position 25mm below the surface layer of the hammer head in example 1, which is distributed among the laths.

Fig. 4 is a comparison of the impact wear weight loss of the hammer head of the present invention and the comparative high manganese steel hammer head.

Detailed Description

The preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form a part hereof, and which together with the embodiments of the invention serve to explain the principles of the invention.

The invention provides an impact wear resistant multiphase structure hammer, the microstructure of which comprises bainite, martensite and retained austenite. Wherein, the microstructure 10mm below the surface layer of the hammer comprises 15 to 30 percent of sheet bainite and 3 to 8 percent of residual austenite according to volume fraction, and the balance is martensite; the microstructure at the position 25mm below the surface layer of the hammer head comprises 5-10% of sheet bainite, 35-50% of lath-shaped bainite and 5-15% of residual austenite in percentage by volume, and the balance of martensite, wherein the martensite is derived from a martensite/austenite island. Specifically, the effects and the content of the microstructures at different parts of the hammer head are designed as follows:

the microstructure design is mainly flaky bainite and martensite at the position 10mm below the surface layer of the hammer. The flaky bainite is formed at a lower temperature in the continuous cooling process, has small size, and has two main functions, wherein the small size of the flaky bainite can ensure the toughness matching of steel, and the formation of the flaky bainite can divide the original austenite grain size and refine the martensite structure formed subsequently. The content design of the flaky bainite is determined according to the phase transformation characteristics, if flaky bainite with more volume fractions is obtained, the cooling speed of a hammer head needs to be controlled in a lower bainite phase transformation area, an additional treatment process is added, and the volume fraction of subsequent martensite is limited by more flaky bainite, so that the volume fraction of the flaky bainite is controlled to be 15-20%. The main purpose of martensite introduction is to increase the hardness of the steel, so that the part is designed to introduce more martensite. As described above, the martensite formed in the same austenite grain is small in size due to the restriction effect of the first formation of the sheet bainite. The fine sheet bainite and martensite structures are beneficial to maintaining high impact toughness of the part of the hammer head while having high strength, thereby resisting impact abrasion damage. The part of the hammer head is reserved with a certain volume fraction of the retained austenite, and the improvement of the impact wear resistance of the hammer head by the retained austenite mainly comprises two aspects, namely, the retained austenite is subjected to martensite phase transformation under the action of an impact load, the newly formed martensite improves the hardness of a wear surface layer, namely, the existence of the retained austenite is beneficial to improving the work hardening performance of the hammer head, so that the impact wear resistance of the hammer head is improved. On the other hand, the improvement of the impact wear resistance of the material not only requires that the material has higher hardness, but also has good toughness, and the existence of the residual austenite can obviously improve the impact toughness of the steel, thereby further improving the impact wear resistance of the hammer head. However, an excessive residual austenite content causes a significant decrease in the initial hardness of the steel. Therefore, the content of the residual austenite at the part of the hammerhead is controlled to be 3-8%.

And the lath-shaped bainite is introduced into the position 25mm below the surface layer of the hammer head through microstructure design. Lath bainite comprises bainitic ferrite and membranous austenite distributed among its laths. The content of lath bainite is regulated and controlled by controlling the termination temperature of the rapid cooling stage. Bainitic ferrite exhibits a good hardening effect due to an increase in dislocation density and refinement in size during impact wear. The membranous residual austenite distributed among the bainite ferrite laths not only improves the toughness matching of the hammer head, but also improves the work hardening performance of the hammer head through the martensite transformation generated under the action of impact load, the content design of the lath bainite is determined according to the phase transformation characteristics, and the lath bainite is generated in a higher temperature range, which is different from the flaky bainite. When the bainite phase transformation is cooled slowly in a higher temperature range, the lath-shaped bainite can be obtained. The content of lath bainite is regulated and controlled by controlling the termination temperature of the rapid cooling stage. The volume fraction of lathy bainite at the part of the hammer head is 35-50%. Meanwhile, 5-15% of retained austenite is retained at the part of the hammer head, and the effect of the retained austenite is as described above. The retained austenite mainly includes film-like and block-like shapes. The film-shaped retained austenite has fine size, high carbon-rich degree and higher mechanical stability. The martensite transformation can continuously occur within a longer time and a larger impact load range in the impact abrasion process, thereby being beneficial to the improvement of the processing and hardening capacity of the hammer head. The massive austenite is insufficient in carbon content and low in mechanical stability, and in the impact wear process, the massive austenite is easy to generate martensite transformation in a short time, so that the improvement effect on the impact wear resistance of the hammer head is limited. Therefore, in the subsequent design of the invention, after quenching is finished, the tempering process is added, and the supersaturated carbon atoms in the bainitic ferrite or martensite are distributed into austenite through tempering and heat preservation, so that the mechanical stability of the block austenite is improved.

Illustratively, the alloy raw materials of the impact and wear resistant complex phase structure hammer head comprise the following components in percentage by mass: 0.25 to 0.45wt.% of C, 1.8 to 2.2wt.% of Mn1.3 to 1.7wt.% of Si, 0.6 to 1.0wt.% of Cr0.1 to 0.45wt.% of Mo0.1 to 0.45wt.%, and the balance of Fe and inevitable impurities.

Specifically, the impact wear resistant complex phase structure hammer head comprises the following components in alloy raw materials:

c element: the strength and the hardness of the hammer head are ensured. When the strength or hardness of the steel is required to be high, a high carbon content is required, but an excessively high carbon content deteriorates the toughness of the steel.

Mn element: the method can remarkably delay the high-temperature phase transformation, has small influence on the bainite phase transformation in the middle-temperature region, and therefore, the cooling rate range of the bainite transformation in the steel can be expanded by adding a proper amount of Mn. However, when the Mn element is too high, segregation tends to increase in the ingot.

Si element: and cementite is inhibited from being precipitated from the untransformed austenite in the phase transformation process, so that the content and the stability of the residual austenite in the steel are improved. Particularly, when the content of the Si element is small, the suppression effect thereof is not significant, and therefore, the Si element mass% in the present invention is 1.3 to 1.7wt.%.

Cr element: on the one hand, the hardenability of the steel can be improved, and on the other hand, the bainite transformation temperature can be reduced, so that a finer bainite structure can be obtained in a wider cooling rate range. However, if the Cr content is too high, carbides such as Cr7C3 are easily formed in the steel, and the ductility and toughness of the steel are deteriorated.

Mo element: improve the tempering stability of the steel and reduce or inhibit the tempering brittleness caused by the segregation of impurity elements in grain boundaries.

The invention also provides a preparation method of the impact wear resistant complex phase structure hammer head, which comprises the following steps:

step 2: processing the cast ingot into a hammer head;

and step 3: carrying out homogenization treatment on the hammer head to reduce the phenomenon of uneven distribution of alloy elements in the casting process;

and 4, step 4: speed and temperature control quenching: reheating and austenitizing the homogenized hammerhead at 880-930 ℃ for 60-90 min to obtain all austenite tissues, and quenching and cooling the hammerhead to room temperature after discharging;

and 5: distribution-stress relief tempering: tempering the quenched hammer at 250-350 ℃, keeping the temperature for 2-4 h, and cooling to room temperature after discharging to obtain the impact-abrasion-resistant complex phase structure hammer.

In step 3, the homogenization treatment includes the following steps:

heating the hammer to 1000-1100 deg.c and maintaining for 8-12 hr.

In step 4, the quenching cooling includes the following steps in order to refine martensite:

rapidly cooling to below 400 ℃ at a cooling rate of 1-30 ℃, and slowly cooling to room temperature at a cooling rate of 0.1-0.5 ℃/s. And (3) rapidly cooling to a temperature close to but higher than the martensite start transformation temperature in the first stage after discharging, so that the part of the hammer head close to the surface layer firstly obtains flaky bainite in the continuous cooling process, divides original austenite grains, and refines martensite formed later. After the material is discharged from the furnace, the material is slowly cooled in the second stage, so that the martensite transformation process at the 10mm position of the hammer head is carried out in a longer time, and the concentration of thermal stress and phase change stress caused by the over-high cooling speed of the surface layer is avoided; on the other hand, the lower 25mm of the surface layer of the hammer head is in a higher bainite transformation temperature range to obtain a lath-shaped bainite structure, and meanwhile, a part of untransformed austenite is reserved.

Illustratively, the rapid cooling medium in the first stage after tapping is water, water mist or strong wind, and the slow cooling mode in the second stage after tapping is stack cooling or cooling in a sand pile.

Compared with the prior art, the preparation method of the impact wear resistant complex phase structure hammer head provided by the invention has the advantages basically the same as those of the impact wear resistant complex phase structure hammer head, and is not repeated herein.

The following describes in detail examples of the present invention, and the alloy raw material compositions of examples 1 to 3 of the present invention are shown in Table 1.

TABLE 1 compositions (in% by mass) of alloy raw materials of examples 1 to 3

Composition (I)	Example 1	Example 2	Example 3
				C	0.32	0.25	0.45
Mn	2.1	2.2	1.8
				Si	1.5	1.3	1.7
Cr	0.7	0.6	1.0
				Mo	0.2	0.45	0.10

The preparation method adopted by the embodiment of the invention comprises the following steps:

step a: smelting, deoxidizing, deslagging and casting the alloy raw material to obtain a cast ingot;

step b: processing the cast ingot into a hammer head;

step c: heating the hammer to 1000-1100 ℃, preserving heat for 8-12 h, and carrying out homogenization treatment on the hammer;

step d: re-austenitizing the hammer head after homogenization treatment, wherein the heating temperature is 880-930 ℃, the heat preservation time is 60-90 min, the hammer head is rapidly cooled to below 400 ℃ at the cooling speed of 1-30 ℃ after being taken out of the furnace, and then is slowly cooled to the room temperature at the cooling speed of 0.1-0.5 ℃/s;

step e: tempering the quenched hammer at 250-350 ℃, keeping the temperature for 2-4 h, and naturally cooling to room temperature after discharging to obtain the impact-abrasion-resistant complex phase structure hammer.

See table 2 for process parameters in the preparation methods of examples 1-3 of the present invention.

Table 2 process parameters in the preparation of examples 1 to 3

The complex phase structure hammer head of example 1 was subjected to microstructure test, and referring to fig. 1 to 3, specific contents and mechanical properties of the microstructures of examples 1 and 3 are shown in tables 3 and 4.

The shape of the microstructure 10mm below the surface layer of the hammer head is shown in figure 1, and as can be seen from figure 1, the microstructure 10mm below the surface layer of the hammer head is mainly flaky bainite and martensite; the microstructure morphology of the part 25mm below the surface layer of the hammer head is shown in fig. 2, and as can be seen from fig. 2, the microstructure of the part 25mm below the surface layer of the hammer head mainly comprises sheet bainite, lath bainite and martensite/austenite islands; the retained austenite distributed among the laths 25mm below the surface layer of the hammer head is shown in fig. 3.

The volume fraction of the retained austenite is measured by an X-ray diffractometer, and the content of the rest microstructures is obtained according to the metallographic structure statistics. The mechanical properties of the wheels of examples 1 and 3 were measured by a SUNS5305 tensile tester and a JB-30A impact tester. Wherein the tensile test size is an M12 standard sample with a gauge length of 25mm, and the impact test sample is a U-shaped notch standard sample with a size of 10mm multiplied by 55 mm.

Table 3 shows the microstructure content and mechanical properties of different parts in example 1

Table 4 shows the microstructure content and mechanical properties of different parts in example 3

As can be seen from tables 3 and 4, the strength of the specimen at 25mm was reduced but the impact toughness was improved compared with the specimen at 10mm for the same multiphase hammer head. The tensile strength of 10mm is 1620-1740 MPa, the yield strength is 1280-1300 MPa, the Rockwell hardness is 48-50 HRC, and the impact energy is 34-55J; the tensile strength at the position of 25mm is 1510-1580 MPa, the yield strength is 1190-1230 MPa, the Rockwell hardness is 45-46 HRC, and the impact energy is 45-64J.

In order to compare the impact wear resistance of the complex phase structure hammer head with the existing high manganese steel hammer head, an MLD-10 type dynamic load impact abrasive wear testing machine is utilized to compare the wear loss under the impact condition of the two hammer heads. The size of an impact sample is 10mm multiplied by 30mm, and the impact sample is taken from a part 10mm below the surface layer of the hammer head; the impact load is 1-4J; the impact frequency was 200 per minute; the impact time was 60min.

The test result is shown in fig. 4, when the impact load is lower (1-3J), the weight average of the abrasion loss of the two hammerheads is reduced along with the increase of the impact load, and the abrasion weight loss of the complex phase structure hammerhead is less than that of the high manganese steel hammerhead, so that the complex phase structure hammerhead has better abrasion resistance under the condition of lower impact load. The abrasion loss of the hammer head under a smaller impact load is lower than that of the traditional high manganese steel, and the selection system of the wear-resistant material under the medium and low load impact condition is enriched.

The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention.

Claims

1. The impact-abrasion-resistant complex phase structure hammer head is characterized in that a microstructure 10mm below the surface layer of the hammer head comprises 15-30% of sheet bainite and 3-8% of residual austenite in percentage by volume, and the balance is martensite;

the microstructure at the position 25mm below the surface layer of the hammer head comprises 5-10% of sheet bainite, 35-50% of lath-shaped bainite and 5-15% of residual austenite in percentage by volume, and the balance is martensite;

the alloy raw materials of the impact-abrasion-resistant complex phase structure hammer head comprise the following components in percentage by mass: c

0.25-0.45 wt.%, mn 1.8-2.2 wt.%, si 1.3-1.7 wt.%, cr 0.6-1.0 wt.%, and Mo0.1-0.45 wt.%, with the balance being Fe and unavoidable impurities.

2. The impact-abrasion-resistant complex phase tissue hammer head according to claim 1, wherein the tensile strength at 10mm is 1620-1740 MPa, the yield strength is 1280-1300 MPa, the Rockwell hardness is 48-50 HRC, and the impact energy is 34-55J; the tensile strength at the position of 25mm is 1510-1580 MPa, the yield strength is 1190-1230 MPa, the Rockwell hardness is 45-46 HRC, and the impact energy is 45-64J.

3. A method for preparing an impact wear resistant complex phase structure hammer head, which is used for preparing the impact wear resistant complex phase structure hammer head as claimed in claim 1 or 2, and comprises the following steps:

step 2: processing the cast ingot into a hammer head;

and step 3: carrying out homogenization treatment on the hammer head;

4. The method for manufacturing the impact-wear-resistant complex phase structure hammer head according to claim 3, wherein in the step 3, the homogenization treatment comprises the following steps:

the hammer is heated to 1000-1100 ℃ and the temperature is kept for 8-12 h.

5. The method for preparing the impact and wear resistant complex phase structure hammer head according to claim 3, wherein in the step 4, the heating temperature is 880-930 ℃.

6. The method for preparing the impact wear resistant complex phase structure hammer head according to claim 3, wherein in the step 4, the heat preservation time is 60-90 min.

7. The method for manufacturing the anti-impact-abrasion complex phase structure hammer head according to claim 3, wherein in the step 4, the cooling comprises the following steps:

8. The method for manufacturing the impact-wear-resistant complex phase structure hammer head according to claim 3, wherein in the step 5, the tempering temperature is 250-350 ℃.

9. The method for preparing the impact wear resistant complex phase structure hammer head according to claim 3, wherein in the step 5, the heat preservation time is 2-4 hours.