CN111996469A - High-hardness ferroalloy and preparation method and application thereof - Google Patents
High-hardness ferroalloy and preparation method and application thereof Download PDFInfo
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- CN111996469A CN111996469A CN202010877297.5A CN202010877297A CN111996469A CN 111996469 A CN111996469 A CN 111996469A CN 202010877297 A CN202010877297 A CN 202010877297A CN 111996469 A CN111996469 A CN 111996469A
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- 229910001021 Ferroalloy Inorganic materials 0.000 title claims abstract description 109
- 238000002360 preparation method Methods 0.000 title claims abstract description 15
- 238000005496 tempering Methods 0.000 claims description 68
- 239000000463 material Substances 0.000 claims description 27
- 238000010791 quenching Methods 0.000 claims description 21
- 230000000171 quenching effect Effects 0.000 claims description 21
- 238000001816 cooling Methods 0.000 claims description 19
- 238000003723 Smelting Methods 0.000 claims description 7
- 238000000034 method Methods 0.000 claims description 7
- 239000002994 raw material Substances 0.000 claims description 6
- 238000005242 forging Methods 0.000 claims description 4
- 238000004519 manufacturing process Methods 0.000 claims 1
- 229910045601 alloy Inorganic materials 0.000 abstract description 15
- 239000000956 alloy Substances 0.000 abstract description 15
- 238000010521 absorption reaction Methods 0.000 abstract description 7
- 238000010438 heat treatment Methods 0.000 description 27
- 239000011651 chromium Substances 0.000 description 12
- 229910000831 Steel Inorganic materials 0.000 description 11
- 239000010959 steel Substances 0.000 description 11
- 229910000640 Fe alloy Inorganic materials 0.000 description 9
- 230000000052 comparative effect Effects 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 229910052799 carbon Inorganic materials 0.000 description 5
- 239000002826 coolant Substances 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 238000004321 preservation Methods 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 4
- 229910001063 inconels 617 Inorganic materials 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 229910052804 chromium Inorganic materials 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 229910052750 molybdenum Inorganic materials 0.000 description 3
- 229910052698 phosphorus Inorganic materials 0.000 description 3
- 239000000047 product Substances 0.000 description 3
- 239000011435 rock Substances 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910052720 vanadium Inorganic materials 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- CWYNVVGOOAEACU-UHFFFAOYSA-N Fe2+ Chemical compound [Fe+2] CWYNVVGOOAEACU-UHFFFAOYSA-N 0.000 description 2
- 229910003178 Mo2C Inorganic materials 0.000 description 2
- 229910052729 chemical element Inorganic materials 0.000 description 2
- 238000010276 construction Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000005098 hot rolling Methods 0.000 description 2
- 229910000734 martensite Inorganic materials 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 229910052759 nickel Inorganic materials 0.000 description 2
- 230000002035 prolonged effect Effects 0.000 description 2
- 230000000630 rising effect Effects 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 230000008542 thermal sensitivity Effects 0.000 description 2
- 238000007550 Rockwell hardness test Methods 0.000 description 1
- 230000018199 S phase Effects 0.000 description 1
- 238000009412 basement excavation Methods 0.000 description 1
- UFGZSIPAQKLCGR-UHFFFAOYSA-N chromium carbide Chemical compound [Cr]#C[Cr]C#[Cr] UFGZSIPAQKLCGR-UHFFFAOYSA-N 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 229910052739 hydrogen Inorganic materials 0.000 description 1
- 238000009863 impact test Methods 0.000 description 1
- 239000012535 impurity Substances 0.000 description 1
- 230000005764 inhibitory process Effects 0.000 description 1
- 239000007769 metal material Substances 0.000 description 1
- 239000000203 mixture Substances 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000006911 nucleation Effects 0.000 description 1
- 238000010899 nucleation Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 229910052700 potassium Inorganic materials 0.000 description 1
- 239000002244 precipitate Substances 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 230000000717 retained effect Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000010998 test method Methods 0.000 description 1
- 229910003470 tongbaite Inorganic materials 0.000 description 1
- 230000009466 transformation Effects 0.000 description 1
- 230000005641 tunneling Effects 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
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
- C22C38/18—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
- 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
- C21D1/56—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering characterised by the quenching agents
- C21D1/58—Oils
-
- 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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/22—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for drills; for milling cutters; for machine cutting tools
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
-
- E—FIXED CONSTRUCTIONS
- E21—EARTH OR ROCK DRILLING; MINING
- E21D—SHAFTS; TUNNELS; GALLERIES; LARGE UNDERGROUND CHAMBERS
- E21D9/00—Tunnels or galleries, with or without linings; Methods or apparatus for making thereof; Layout of tunnels or galleries
- E21D9/06—Making by using a driving shield, i.e. advanced by pushing means bearing against the already placed lining
- E21D9/08—Making by using a driving shield, i.e. advanced by pushing means bearing against the already placed lining with additional boring or cutting means other than the conventional cutting edge of the shield
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Crystallography & Structural Chemistry (AREA)
- Thermal Sciences (AREA)
- Physics & Mathematics (AREA)
- Mining & Mineral Resources (AREA)
- Oil, Petroleum & Natural Gas (AREA)
- Environmental & Geological Engineering (AREA)
- Life Sciences & Earth Sciences (AREA)
- General Life Sciences & Earth Sciences (AREA)
- Geochemistry & Mineralogy (AREA)
- Geology (AREA)
- Heat Treatment Of Steel (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
The invention belongs to the technical field of alloys, and particularly relates to a high-hardness ferroalloy, and a preparation method and application thereof. The invention provides a high-hardness ferroalloy which comprises the following element components in percentage by mass: 0.48-0.54% of C, 3.8-4.3% of Cr, 1.8-2.2% of Ni, 1.1-1.75% of Mo, 0.8-1.2% of Si, 0.8-1.2% of V, 0.4-0.6% of Mn, 0-0.03% of P, 0-0.03% of S and the balance of Fe. The high-hardness ferroalloy provided by the invention has certain toughness, and simultaneously improves the hardness of the high-hardness ferroalloy, so that the high-hardness ferroalloy has wear resistance. The example results show that the hardness of the high-hardness ferroalloy provided by the invention is 58-61 HRC, and the impact absorption work is 15-17J.
Description
Technical Field
The invention belongs to the technical field of alloys, and particularly relates to a high-hardness ferroalloy, and a preparation method and application thereof.
Background
The shield machine is special for the ultra-large mechanical equipment for hard rock layer tunneling, and utilizes a replaceable disc cutter fixed on a cutter head to penetrate and roll rocks so as to gradually penetrate through a tunnel. The cutter ring is used as the most critical consumable material of the shield machine with the largest use amount, and the use cost of the cutter ring can account for one third of the total cost of tunnel construction. When the construction is carried out under the geological condition of hard rock, the cutter ring of the shield machine needs to bear violent impact and friction, so that the cutter ring is easy to wear and break and lose efficacy.
At present, the mainstream shield machine cutter ring material is derived steel grade H13(4Cr5MoSiV1), however, with the development of the tunnel excavation engineering project in China, higher requirements are provided for the hardness and the wear resistance of the cutter ring, so that the service life of the cutter ring is prolonged, the working efficiency is improved, and the use cost is reduced.
Disclosure of Invention
In view of the above, the invention provides a high-hardness ferroalloy, which improves the hardness of the alloy on the basis of ensuring that the alloy has certain toughness, has higher wear resistance, and can prolong the service life of a shield machine cutter ring and reduce the cost by using the high-hardness ferroalloy for preparing the shield machine cutter ring.
The invention provides a high-hardness ferroalloy which comprises the following element components in percentage by mass:
preferably, the high-hardness iron alloy comprises the following element components in percentage by mass:
the invention also provides a preparation method of the high-hardness ferroalloy in the technical scheme, which comprises the following steps:
smelting and forging the high-hardness ferroalloy raw material in sequence according to the mass ratio of elements to obtain a blank material;
quenching the blank material to obtain a primary high-hardness ferroalloy;
and tempering the primary high-hardness ferroalloy for at least three sections to obtain the high-hardness ferroalloy.
Preferably, the quenching temperature is 1040-1080 ℃ and the quenching time is 20-40 min.
Preferably, the heating rate of the temperature rising to the quenching temperature is 5-15 ℃/min.
Preferably, the quenching cooling medium is oil, the oil comprises mechanical oil, and the model of the mechanical oil is L-AN20 or L-AN 30.
Preferably, when the tempering is three-stage tempering, the three-stage tempering sequentially comprises a first tempering, a second tempering and a third tempering, wherein the temperature of the first tempering is 530-550 ℃, the temperature of the second tempering is 510-530 ℃, and the temperature of the third tempering is 490-510 ℃; in the three-stage tempering, the tempering time of each stage is independently 120-150 min.
Preferably, the temperature rise rate of each tempering section is 5-15 ℃/min independently.
Preferably, each section further comprises, after tempering: and respectively cooling the tempered products of each section to room temperature in air.
The invention also provides application of the high-hardness ferroalloy in the technical scheme or the high-hardness ferroalloy prepared by the preparation method in the technical scheme in a shield machine cutter ring.
The invention provides a high-hardness ferroalloy which comprisesThe material comprises the following element components in percentage by mass: 0.48-0.54% of C, 3.8-4.3% of Cr, 1.8-2.2% of Ni, 1.1-1.75% of Mo, 0.8-1.2% of Si, 0.8-1.2% of V, 0.4-0.6% of Mn, 0-0.03% of P, 0-0.03% of S and the balance of Fe. The high-hardness ferroalloy provided by the invention contains high content of C, so that the hardness of the high-hardness ferroalloy is improved; the Cr with the mass percentage can promote the high-hardness ferroalloy to be completely quenched, and the hardness of the high-hardness ferroalloy is also improved; the Mn with the mass percentage can furthest improve the wear resistance of the high-hardness ferroalloy under the condition of ensuring that the thermal sensitivity of the high-hardness ferroalloy is controllable. According to the invention, the Si can strengthen the high-hardness ferroalloy matrix, increase the hardenability of the high-hardness ferroalloy and improve the thickness of the wear-resistant layer. The Mo and the V can form Mo with C2C. VC, said Mo2C. VC can refine grains of the high-hardness ferroalloy and improve the red hardness of the high-hardness ferroalloy. The high-hardness ferroalloy provided by the invention ensures that the high-hardness ferroalloy has certain toughness under the combined action of the components in percentage by mass, improves the hardness of the high-hardness ferroalloy, enables the high-hardness ferroalloy to have higher wear resistance, can be used as a material of a cutter ring of a shield machine, prolongs the service life of the cutter ring, and reduces the use cost of the shield machine. The example results show that the hardness of the high-hardness ferroalloy provided by the invention is 58-61 HRC, and the impact absorption work is 15-17J.
The invention also provides a preparation method of the high-hardness ferroalloy in the technical scheme, which comprises the following steps: smelting and forging the high-hardness ferroalloy raw material in sequence to obtain a blank material; quenching the blank material to obtain a primary high-hardness ferroalloy; and tempering the primary high-hardness ferroalloy for at least three sections to obtain the high-hardness ferroalloy. The preparation method provided by the invention is simple and easy to operate. In the invention, the quenching takes oil as a cooling medium, so that the cooling deformation and cracking tendency of the high-hardness ferroalloy can be reduced; multi-stage tempering enables the Mo2C. VC is precipitated to obtain the effect of secondary hardening and refine the grain structure of the high-hardness ferroalloy, so that the high-hardness ferroalloy has higher hardness and keeps certain toughness of the high-hardness ferroalloy。
Detailed Description
The invention provides a high-hardness ferroalloy which comprises the following element components in percentage by mass:
in the present invention, all the raw material components are commercially available products well known to those skilled in the art, unless otherwise specified.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 0.48-0.54% of C, preferably 0.5-0.51%. When the carbon content in the alloy is below 0.6%, the strength and hardness of the alloy are improved along with the increase of the carbon content, and simultaneously the brittleness of the alloy is also improved.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 3.8-4.3% of Cr, and preferably 4-4.1%. In the invention, the Cr is used as a carbide forming element, so that the nucleation growth of the carbide during phase change can be prevented, and the hardenability of the high-hardness ferroalloy is improved; the chromium carbide formed by the Cr has higher stability, is not easy to grow up, can refine crystal grains and improve the strength of the high-hardness ferroalloy; meanwhile, during tempering, Cr can prevent M3C type carbide from growing, and the tempering stability is improved.
In the present invention, the Cr in the above content range can improve the tempering stability, hardenability and hardenability of the high hardness ferrous alloy, and improve the wear resistance of the high hardness ferrous alloy.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 1.8-2.2% of Ni, and preferably 1.9-2%. In the present invention, Ni is an austenite forming element, and can reduce the dislocation motion resistance in the high-hardness iron alloy, relax the stress, and improve the matrix toughness of the high-hardness iron alloy.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 1.1-1.75% of Mo, and preferably 1.5-1.7%. In the present invention, the Mo is capable of forming Mo with C2And C, refining the grain structure of the high-hardness ferroalloy so as to improve the hardenability and the heat strength of the high-hardness ferroalloy, so that the high-hardness ferroalloy keeps enough strength and creep resistance at high temperature, and the hardness of the high-hardness ferroalloy is improved.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 0.8-1.2% of Si, and preferably 1-1.1%. In the present invention, Si has a strong solid-solution strengthening effect as a ferrite-forming element, and can improve the strength of steel.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 0.8-1.2% of V, and preferably 0.9-1%. In the invention, the V is used as a strong carbide forming element and can form VC with good particle stability with C, and the VC is dispersed in the high-hardness ferroalloy and can play a fine-grain strengthening effect so as to improve the hardness of the high-hardness ferroalloy.
According to the mass percentage, the high-hardness ferroalloy provided by the invention comprises 0.4-0.6% of Mn, and preferably 0.45-0.5%. In the present invention, Mn has a good solid solution strengthening effect in the high hardness iron alloy as the strengthening ferrite, and can effectively improve the strength of the high hardness iron alloy, stabilize the retained austenite phase, lower the Ms point to expand the 's phase region, increase the hardenability of the steel, and provide the high hardness iron alloy with a certain toughness. The Mn element can be dissolved into the carbide to inhibit the coarsening of the carbide at high temperature, and the higher the inhibition capability of the Mn element is along with the increase of the temperature and the prolonging of the heat preservation time, the better the thermal stability is. Within the content range, the hardness of the high-hardness ferroalloy can be improved while the thermal sensitivity of the high-hardness ferroalloy is in an adjustable range, so that the wear resistance of the high-hardness ferroalloy is improved.
According to the mass percentage, the high-hardness iron alloy provided by the invention comprises 0-0.03% of P, preferably 0.004-0.009%, and also comprises 0-0.03% of S, preferably 0.005-0.007%. In the present invention, P and S are inevitable impurity elements.
According to the mass percentage, the high-hardness ferroalloy provided by the invention also comprises the balance of Fe.
The invention limits the content of each element in a specific range, and improves the hardness of the high-hardness ferroalloy while ensuring that the high-hardness ferroalloy has certain toughness under the combined action of each element.
The invention also provides a preparation method of the high-hardness ferroalloy in the technical scheme, which comprises the following steps:
according to the technical scheme, the high-hardness ferroalloy raw material is sequentially smelted and forged according to the element mass ratio of the high-hardness ferroalloy to obtain a blank material;
quenching the blank material to obtain a primary high-hardness ferroalloy;
and tempering the primary high-hardness ferroalloy for at least three sections to obtain the high-hardness ferroalloy.
According to the technical scheme, the high-hardness ferroalloy raw material is sequentially smelted and forged to obtain a blank material. The source of the high-hardness ferroalloy element component is not particularly limited in the present invention, and materials well known in the art may be used. The smelting mode is not specially limited, and the conventional smelting mode is adopted. The forging method is not particularly limited, as long as a preliminarily formed blank material can be obtained.
After obtaining the blank material, quenching the blank material to obtain the primary high-hardness ferroalloy. In the invention, the quenching temperature is preferably 1040-1080 ℃, more preferably 1050-1060 ℃, and the heating rate of heating to the quenching temperature is preferably 5-15 ℃/min, more preferably 10 ℃/min; the quenching heat preservation time is preferably 20-40 min, and more preferably 25-30 min.
In the present invention, the quenching cooling medium is preferably oil, the oil preferably comprises mechanical oil, and the type of the mechanical oil is preferably L-AN20 or L-AN 30. The invention takes oil as cooling medium, and preferably cools the blank material after heat preservation to room temperature.
In the present invention, the cooling process in the quenching is preferably to cool the blank material after the heat preservation to room temperature. In the invention, the heat preservation treatment in the quenching process enables the alloy to become austenitized and prepares for subsequent cooling and phase transformation to obtain a martensite phase; mo and V will also form Mo with C2C and VC can strengthen the hardness of the alloy. The invention changes austenite into martensite structure through cooling, and improves the hardness of the alloy. The invention takes oil as cooling medium, which can reduce the tendency of cooling deformation and cracking of the alloy, improve the stability of the alloy structure and further ensure the mechanical property of the alloy.
After the primary high-hardness ferroalloy is obtained, the invention performs at least three-stage tempering on the primary high-hardness ferroalloy to obtain the high-hardness ferroalloy. In the invention, when the tempering is a three-stage tempering, the three-stage tempering preferably comprises a first tempering, a second tempering and a third tempering, the temperature of the first tempering is preferably 530-550 ℃, the temperature of the second tempering is preferably 510-530 ℃, and the temperature of the third tempering is preferably 490-510 ℃. In the present invention, the temperature of the second tempering is preferably 20 ℃ lower than the temperature of the first tempering, and the temperature of the third tempering is preferably 20 ℃ lower than the temperature of the second tempering. The temperature rise rate of each tempering section is preferably 5-15 ℃/min independently, and more preferably 10 ℃/min; the temperature rising rate of tempering in each section is preferably the same; in the three-stage tempering, the tempering time of each stage is preferably 120-150 min independently, and more preferably 125-130 min; the time for each tempering is preferably the same.
In the invention, the residual austenite content in the high-hardness ferroalloy can be reduced through the three-stage tempering treatment so as to increase the hardness of the high-hardness ferroalloy; simultaneously, Mo generated in the three-stage tempering and quenching process2C and VC precipitate to have the effect of secondary hardening.
According to the invention, the product after each stage of tempering is preferably independently cooled to room temperature by air.
The invention also provides application of the high-hardness ferroalloy in the technical scheme or the high-hardness ferroalloy prepared by the preparation method in the technical scheme in preparation of the shield machine cutter ring. The invention has no special requirements on the size of the cutter ring of the shield machine, and is set according to actual requirements, and in the embodiment of the invention, the diameter of the cutter ring of the shield machine is 432mm, and the thickness of the cutter ring of the shield machine is 76 mm. The high-hardness ferroalloy provided by the invention has higher hardness while keeping certain toughness, and can be used under the harsh condition of high hardness.
The technical solutions provided by the present invention are described in detail below with reference to examples, but they should not be construed as limiting the scope of the present invention.
Example 1
According to the mass percentage, 0.5 percent of C, 4 percent of Cr, 2 percent of Ni, 1.5 percent of Mo, 1 percent of Si, 1 percent of V, 0.5 percent of Mn, 0.004 percent of P, 0.005 percent of S and 89.491 percent of Fe are smelted, and then are hot-rolled into blank materials with the diameter of 432mm and the thickness of 76 mm;
heating the blank material to 1050 ℃ at the heating rate of 10 ℃/min, and keeping the temperature for 30 min; then cooling by using mechanical oil with the model number of L-AN20 to obtain a primary high-hardness ferroalloy;
heating the primary high-hardness ferroalloy to 530 ℃ at a heating rate of 10 ℃/min, preserving the temperature for 120min, performing first tempering, and then air-cooling to room temperature;
heating the ferroalloy which is air-cooled to room temperature after the first tempering to 510 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, carrying out second tempering, and then air-cooling to room temperature;
and (3) heating the ferroalloy which is air-cooled to room temperature after the second tempering to 490 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, and then air-cooling to room temperature to obtain the high-hardness ferroalloy.
Example 2
Smelting 0.5% of C, 4% of Cr, 2.2% of Ni, 1.5% of Mo, 0.8% of Si, 1.2% of V, 0.5% of Mn, 0.004% of P, 0.005% of S and 89.291% of Fe in percentage by mass, and hot-rolling the smelted materials into blank materials with the diameter of 432mm and the thickness of 76 mm;
heating the blank material to 1055 ℃ at a heating rate of 10 ℃/min, and preserving heat for 20 min; then, cooling by using mechanical oil with the model of L-AN30 to room temperature to obtain primary high-hardness ferroalloy;
heating the primary high-hardness ferroalloy to 540 ℃ at a heating rate of 10 ℃/min, preserving the heat for 120min, performing first tempering, and then cooling the primary high-hardness ferroalloy to room temperature in air;
heating the ferroalloy which is air-cooled to room temperature after the first tempering to 520 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, carrying out second tempering, and then air-cooling to room temperature;
and (3) heating the ferroalloy which is air-cooled to room temperature after the second tempering to 500 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, and then air-cooling to room temperature to obtain the high-hardness ferroalloy.
Example 3
Smelting 0.5% of C, 4% of Cr, 1.8% of Ni, 1.7% of Mo, 1.2% of Si, 1.2% of V, 0.6% of Mn, 0.009% of P, 0.007% of S and 88.984% of Fe in percentage by mass, and hot-rolling the smelted materials into blank materials with the diameter of 432mm and the thickness of 76 mm;
heating the blank material to 1060 ℃ at the heating rate of 10 ℃/min, and keeping the temperature for 20 min; then cooling by using mechanical oil with the model of L-AN30 to room temperature to obtain primary high-hardness ferroalloy;
heating the primary high-hardness ferroalloy to 550 ℃ at a heating rate of 10 ℃/min, preserving the heat for 120min, performing first tempering, and then air-cooling to room temperature;
heating the ferroalloy which is air-cooled to room temperature after the first tempering to 530 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, carrying out second tempering, and then air-cooling to room temperature;
and (3) heating the ferroalloy which is air-cooled to room temperature after the second tempering to 510 ℃ at the heating rate of 10 ℃/min, preserving the heat for 120min, and then air-cooling to room temperature to obtain the high-hardness ferroalloy.
Comparative example 1
H13 steel was used as comparative example 1, the H13 steel included the following chemical element composition: 0.419% C, 5.36% Cr, 1.1% Si, 1.4% Mo, 0.827% V, 0.341% Mn, 0.007% P, 0.005% S and 90.541% Fe.
Comparative example 2
The Inconel 617 steel was used as a comparative example 2, and the Inconel 617 steel included the following chemical element components: 0.06% C, 12% Co, 9% Mo, 1.5% Fe, 1.0% Si, 1.0% Al, 22% Cr, 0.4% Ti, 1.0% Mn, 52.04% Ni.
The hardness, impact absorption power and volumetric wear rate of the high-hardness iron alloy prepared in examples 1-3, H13 steel in comparative example 1 and Inconel 617 steel in comparative example 2 were tested according to the test method (scale A, B, C, D, E, F, G, H, K, N, T), the Charpy impact test of GB/T229- & 2007 metal material and the reciprocating wear test of the GB/T230.1 Rockwell hardness test part 1, and the results are shown in Table 1.
Table 1 hardness, impact absorption power, and volumetric wear rate of high-hardness ferroalloys prepared in examples 1 to 3, H13 steel in comparative example 1, and Inconel 617 steel in comparative example 2
Common failure modes of a shield machine cutter ring include worn sharp edges and broken sharp edges. Under the condition of high hardness, the volume wear rate of the cutter ring is obviously reduced, and the friction damage can be effectively reduced. In general, an increase in hardness index is accompanied by a decrease in impact absorption power, and the cutter ring is difficult to relieve the impact load, resulting in chipping and breakage. Therefore, the cutter ring needs good hardness to match with the impact absorption work, so that the volume wear rate of the cutter ring is reduced, and the service life of the cutter ring of the shield machine is prolonged. From table 1, it can be seen that the high-hardness iron alloy provided by the embodiment has extremely high hardness, a low volumetric wear rate, a certain impact absorption power, and a considerable toughness, and can effectively prolong the service life of the cutter ring.
Although the present invention has been described in detail with reference to the above embodiments, it is only a part of the embodiments of the present invention, not all of the embodiments, and other embodiments can be obtained without inventive step according to the embodiments, and the embodiments are within the scope of the present invention.
Claims (10)
1. A high-hardness ferroalloy comprises the following element components in percentage by mass:
2. the high-hardness ferroalloy according to claim 1, comprising the following elemental components in percentage by mass:
3. the method for preparing a high-hardness ferroalloy according to claim 1 or 2, comprising the steps of:
smelting and forging the high-hardness ferroalloy raw material in sequence according to the mass ratio of elements to obtain a blank material;
quenching the blank material to obtain a primary high-hardness ferroalloy;
and tempering the primary high-hardness ferroalloy for at least three sections to obtain the high-hardness ferroalloy.
4. The preparation method according to claim 3, wherein the quenching temperature is 1040-1080 ℃ and the quenching time is 20-40 min.
5. The production method according to claim 4, wherein a temperature rise rate of raising the temperature to the quenching temperature is 5 to 15 ℃/min.
6. The method according to any one of claims 3 to 5, wherein the quenching medium is oil, the oil comprises mechanical oil, and the type of the mechanical oil is L-AN20 or L-AN 30.
7. The preparation method according to claim 3, wherein when the tempering is a three-stage tempering, the three-stage tempering sequentially comprises a first tempering, a second tempering and a third tempering, wherein the temperature of the first tempering is 530-550 ℃, the temperature of the second tempering is 510-530 ℃, and the temperature of the third tempering is 490-510 ℃; in the three-stage tempering, the tempering time of each stage is independently 120-150 min.
8. The preparation method according to claim 7, wherein the temperature rise rate of each stage of tempering is 5-15 ℃/min independently.
9. The method of claim 3, wherein after tempering each stage further comprises: and respectively cooling the tempered products of each section to room temperature in air.
10. Use of the high-hardness ferroalloy according to claim 1 or 2 or the high-hardness ferroalloy prepared by the preparation method according to any one of claims 3 to 9 in a shield machine cutter ring.
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