CN100540714C - A kind of snappiness, high-strength steel and manufacture method thereof - Google Patents
A kind of snappiness, high-strength steel and manufacture method thereof Download PDFInfo
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- CN100540714C CN100540714C CNB2005101240268A CN200510124026A CN100540714C CN 100540714 C CN100540714 C CN 100540714C CN B2005101240268 A CNB2005101240268 A CN B2005101240268A CN 200510124026 A CN200510124026 A CN 200510124026A CN 100540714 C CN100540714 C CN 100540714C
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- 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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
Abstract
A kind of shock-resistant, anti abrasive snappiness, high-strength steel, wherein, described steel contains V, the N of 0.0025-0.02 weight % of Al, 0.05-0.1 weight % of Mo, 0.005-0.04 weight % of Ni, 0.01-0.5 weight % of Cr, 0.01-0.1 weight % of Mn, 1.4-2.4 weight % of Si, 0.5-1.0 weight % of C, the 1.4-2.5 weight % of 0.26-0.48 weight %, remains to be Fe and unavoidable impurities.Shock-resistant, anti abrasive snappiness of the present invention, high-strength steel have high rigidity, high strength, high tenacity and snappiness, and the weldability of steel, low-temperaturetempering resistance and high tempering resistance, sclerosis can, wearability and mechanical characteristicies such as impelling strength and tensile strength are very good, so be used for stringent condition mould life in following time and component life is longer than steel in the past far away.
Description
Technical field
The present invention relates to be applicable to the special steel material and the manufacture method thereof of the industrial parts that use under the stringent condition, described material is used for industrial cutter knife, the wearability parts of various pulverizers, the rock failure blade part, specifically, the present invention relates to be used for industrial cutter knife (pocket knife (knife), stapling machine (cutter), blade (blade) etc.), various (rocks, ore, timber, cereal, cement etc.) the wearability parts (stapling machine of pulverizer, ruling machine (liner), thin plate (plate) etc.), or rock failure blade part-piston (piston), chisel (chisel), drill bit (drill bit) etc. is used to cut off iron waste wood (scrap), stainless steel materials, metal such as copper and aluminum alloy plate materials and nonmetallic and excellent property, the high tenacity that manufacturing cost is lower, the economy material and the manufacture method thereof of high strength and high abrasion resistance, relate to snappiness in more detail, high strength special purpose steel and manufacture method thereof, this method comprises the C by low levels in the suitable mixing, high-load Si, and other alloying elements of low levels, form alloy composite, and suitably carry out modifier treatment (quenching more than 900 ℃ and the tempering below 500 ℃, and controlled chilling), guarantee the shock-resistance and the wearability of steel.
Background technology
Scrap iron cutter blades and stainless steel materials cutter blades are the typical industry parts that need high strength and high tenacity, mainly use hot-work steel SKD61 (more than the hardness HRC45 at present according to its purposes selectivity, more than shock absorption energy 40 Jiao), cold work steel SKD11 (more than the hardness HRC56, more than shock absorption energy 10 Jiao) and improvement steel etc. thereof.European patent EP 3218051A119830203DE discloses the nickelic Cr-Mo-V of high-carbon of high strength cutter knife, and Japanese Patent JP 08027540 discloses to guaranteeing that high rigidity and intensity adds the Ti of C, the 0.01-0.03 weight % of 0.4-0.47 weight %, the heavy carbon boron-containing steel of the Al of 0.015-0.040 weight %, the B of 5-30ppm etc.But above-mentioned steel, according to the manufacturing cost height of purposes and is compared the life-span with manufacturing cost and is lacked owing to be high quality steel.In addition,, can not cut off the desired shape model, be difficult to make complex-shaped parts with oxygen blast because carbon content height and alloy amount height so have self-hardening property, crack (crack) occurs easily, and the expense height.
For overcoming the problems referred to above, at present mainly will in or soft steel (for example low-carbon abrasion resistant decrease steel be that Weldox, medium high carbon Abrasion Resistant Steels are Hardox) be used for the wearability parts (stapling machine, ruling machine, thin plate etc.) etc. of the pulverizer of crushed rock, ore, timber, cereal, cement etc.In Korean Patent 2003-0054423 number the low carbon low silicon non-hardened and tempered steel is disclosed, middle low carbon low silicon Ni-Cr-Mo modifier treatment steel is disclosed for 2003-0002183 number at korean patent application, the wear-resistant steel alloy of medium high carbon is disclosed at Japanese Patent JP 60033339, disclose the low silicon high-chromium wear-resistant of medium high carbon at Japanese Patent JP 11131193 and decreased steel alloy, disclose low wear-resistant boron steel of the high Cr-Mo-Zr-W of silicon of medium high carbon and steel alloy at Japanese Patent JP 05214485 and JP 58153759.But the manufacturing expense of above-mentioned steel is very high.
In addition, Korea S reaches external piston as the rock breaker parts and mainly uses SNCM26V (SNCM616V), its price height, and low-carbon (LC) Ni-Cr-Mo steel need be soaked for a long time carbon and handle (more than 4 days) and subzero treatment, guarantee outside high rigidity and inner high tenacity, chisel and drill bit are guaranteed high rigidity by SCM440 or medium high carbon Ni-Cr-Mo steel are carried out modifier treatment, make it have shock-resistance and wearability, but its life-span is compared with price and can't meet the demands, and these improvement steel are difficult to be extensive use of from performance or manufacturing cost at present.
In addition, in the existing Abrasion Resistant Steels,, high Mn changes owing to producing self.When Mn content surpasses 1.7 weight %, produce low temperature and change resultant, though the intensity of increasing substantially, but sharply reduce unit elongation, and Si/Mn ratio hour in the low alloy steel, cooling changes beginning of (CCT) Medium pearlite/ferrite (pearlite/ferrite) variation and end point reduction continuously, carrying out martensite/bainite (Martensite/Bainite) easily changes, self-hardening property strengthens after the hot-work, be easy to generate the crack, be must the anneal thermal treatment process of (Annealing) of mechanical workout simultaneously.
Summary of the invention
The present invention shock-resistantly occurs the problems referred to above with parts and wearability parts and rock failure blade part etc. very on the industrial part that uses down of stringent condition the time and proposes for what solve that steel in the past is used for industrial cutter knife (stapling machine, blade), various industrial machinery (various pulverizers, shears, spraying machine (shot) etc.).The present invention seeks to provide and have hardness HRC52 and yield strength more than 1350 Ns/square metre by middle low-carbon (LC)/high silicon/low-alloyed appropriate combination and modified heat treating method, tensile strength is more than 1750 Ns/square millimeters, unit elongation is more than 15%, the cross section decrement is more than 35%, has good strength and impelling strength more than shock absorption energy 65 Jiao, good hardening, wearability, particularly have oxygen blast and cut off the model feasibility, good welds shock-resistant, anti abrasive snappiness, high-strength steel and manufacture method thereof.
In addition, the purpose of this invention is to provide shock-resistant, anti abrasive snappiness, high-strength steel and manufacture method thereof.In order to prevent from mechanical characteristics is risen the Al of bad influence
2O
3The independent generation of the nonmetal inserting of MnS, and in order to obtain optimal solidified structure, the present inventor is through studying discovery for a long period of time, utilize the interior rare earth element (to call REM in the following text) of molten steel and the concentration and the solubleness correlationship formula of Al and sulphur, the concentration correlationship formula of calcium and sulphur, in molten steel, generate RExOy or the (RE of diameter below 5 microns, Al) xOy+RExOyS+RExSy complex chemical compound, solidify molten steel, form resin state, inhomogeneous product nucleus environment is provided, make solidified structure miniaturization and densification, powerful simultaneously control C, Cr, Mo, W, Ni, Mn, fusion elements segregation such as Si and fine dispersion obtain mechanical characteristics, shock-resistant/anti abrasive snappiness that physical property and erosion resistance are higher, high-strength steel.
For achieving the above object, shock-resistant, anti abrasive snappiness provided by the invention, high-strength steel have following several composition:
Form 1:
0.26-0.48 the N of the V of the Al of the Mo of the Ni of the Cr of the Mn of the Si of the C of weight %, 1.4-2.5 weight %, 0.5-1.0 weight %, 1.4-2.4 weight %, 0.01-0.1 weight %, 0.01-0.5 weight %, 0.005-0.04 weight %, 0.05-0.1 weight %, 0.0025-0.02 weight %, residue are Fe and unavoidable impurities.
Form 2:
In order to control solidified structure, shock-resistant, anti abrasive snappiness, the high-strength steel of composition 2 contain the REM (Y, Ce, La, Nd, Pr) of the 0.001-0.5 weight % that meets following relational expression 1 and the Ca of 0.0005-0.01 weight %.
The concentration formula:
[REM weight % (Y, Ce, La, Nd, Pr)+Al weight %]/[S weight %]=2-90 and [Ca weight %]/[S weight %]=1.
The solubleness formula:
[REM (Y, Ce, La, Nd, Pr)+Al]/[O+S]=0.001 * 10
-5-30000 * 10
-5[weight %].
Form 3:
In order to improve matrix strength, sclerosis energy and thermal property more, form 3 high-strength steel and be the higher limit of N, Mn at above-mentioned composition 1, Cr, Ni, each composition range of Mo, also contain Ni, the Mo of 0.6 weight % of Cr, 0.95 weight % of Mn, the 1.0 weight % of N, 0.5 weight % that maximum is respectively 0.28 weight %, and preferably also contain W+Co, the Nb of 0.05-0.1 weight % etc. of Ti, 0.01-0.5 weight % of B, the 0.001-0.1 weight % of 0.0001-0.005 weight %.
Form 4:
Forming 1 and form 2 and form in 3, above-mentioned high-strength steel satisfies following relational expression 2:
[Si weight %]/[Mn weight %]=2.6-3.2 and [Al weight %]/[N weight %]=2: 1.
This is modified heat-treated steel crystallization control grain growth at high temperature and generate the optimal condition and range of particles A lN, i.e. [Al weight %]/[N weight %]=2: 1, and add the nitrogen of 0.30 weight % at most in order in cold and hot condition is used, to improve matrix strength more.The Si/Mn ratio is big more, it is easy more that perlite/ferrite changes, and produce stratiform at interval, martensite/bainite is changed be difficult to, under the intermediates state, obtain soft after the hot-work, can economize the slightly annealing heat treatment process of machinability, reduce manufacturing cost, and after oxygen blast cut-out and the welding microscopic checks can not take place yet, bring into play its effect to greatest extent, for this reason with [Si weight %]/[Mn weight %]=2.6-3.2.
In addition, at the problem of modified heat-treated steel owing to hardness after above-mentioned martensite/bainite variation difficulty is difficult to guarantee to quench, the present invention is by replenishing a small amount of Cr and generating high Si, AlN, RExOy or the (RE of diameter below 5 microns, Al) xOy+RExOyS+RExSy complex chemical compound, utilize the precipitate in the crystallization control grain growing system under the high temperature, long-time even heating under high temperature more than 900 ℃, solid fully fusing, and by the rapid water cooling of cooling system and the rapid cooling of water cooling+salt bath, obtaining surface hardness is above high rigidity of HRC56 and stable alternative construction.
Description of drawings
Fig. 1 is the photo that the micro organization of expression high-strength steel of the present invention under quenching temperature and tempering temperature changes;
Fig. 2 is the comparison diagram of the R of steel in the past, the X of invention steel B of the present invention, F, G, P and the prior art changes in hardness situation after by modified thermal treatment;
Fig. 3 is the comparison diagram of wearability of the R of steel in the past, the X of invention steel B of the present invention, P and prior art;
Fig. 4 be invention steel D of the present invention, Q and prior art the R of steel in the past, V, X sclerosis can comparison diagram;
Among Fig. 5,5a is the photo of the scrap iron cutter blades of high-strength steel of the present invention, and 5b is the photo of scrap iron cutter blades of the X of steel in the past of prior art;
Fig. 6 is the photo of the stainless steel materials cutter knife of high-strength steel of the present invention;
Fig. 7 a is the Fe-C phasor (Vertical SectionThermo-Calc.Phase Diagram) that the present invention represents invention steel K when calcining vertical section;
Fig. 7 b is the continuous cooling change curve of foregoing invention steel K.
Embodiment
The bound theorem of the composition range that below chemical ingredients of invention steel is added reason and represent with weight % is by describing.
Carbon (C): 0.26-0.48 weight %
C is the representative element of stable austenite phase, is that contained being used to improves intensity and quenching hardness, guarantees the important element of wearability in matrix.Quench back hardness more than HRC56 in order to ensure steel of the present invention, the add-on of carbon must be not less than 0.26 weight %, if but excessive interpolation, solidify V, Nb, the W combination of Shi Huiyu as the one-time process carbide forming element, mechanical characteristics is had a negative impact, so be limited to below the 0.48 weight %.
Silicon (Si): 1.4-2.5 weight %
Si is a most important element in the manufacturing of snappiness, high-strength steel of the shock-resistant/wearability of the object of the invention, it is the element of reinforced ferrite tissue, when the fusion refining, use as effective de-acidying agent, can also grow by the crystallization control grain simultaneously, improve acid resistance, strengthen 300 ℃ of following low-temperaturetempering resistance, when making castings, strengthen molten steel flowability, reduce surface imperfection.Addition can not get the effect of the Si of requirement of the present invention during less than 1.4 weight %, adds when excessive plastic working is had a negative impact, so be limited to below the 2.5 weight %.
Manganese (Mn): 0.5-1.5 weight %
Mn is the element that improves the sclerosis energy, uses as de-acidying agent, improve the uniformity and the intensity of tissue when thermal treatment, but the tempering resistance is poor, combines with S and improves machinability, prevents red brittleness.Addition can reduce the N solid solubility and can not get above-mentioned effect during less than 0.5 weight %, if excessive interpolation, soaking easily, therefore at the proportional range of the Si/Mn of foregoing invention steel key character, its upper limit is limited to below the 1.5 weight %.
Cr:1.4-3.4 weight %
Cr improves hardenability and tempering resistance, improves intensity and soaks carbon, and form fine carbide, suppresses the crystal grain growth, improves toughness, and improves wearability.Addition is during less than 1.4 weight %, and the quenching hardness that can not produce the Si/Mn limited proportion owing to feature of the present invention reduces and replenishes, and can not get above-mentioned effect, and adds 3.4 weight % when above, forms the Cr carbide on the contrary in a large number, reduction toughness.
Ni:0.01-1.0 weight %
Ni is the very important element that improves impelling strength, can improve the sclerosis energy, and large-scale material hot treatment is become easily, prevents low temperature brittleness, improves erosion resistance.Add when a small amount of, can increase substantially toughness, and add when a large amount of, cost height not only, and form retained austenite, cause embrittlement.Therefore, the interpolation scope is limited to 0.01-1.0 weight %.
Mo:0.01-1.1 weight %
Mo and Cr form stable double carbide, improve the tempering resistance, improve the sclerosis energy.Mo is the foregoing invention steel after thermoplasticity processing, the important element that the control tissue changes during quenching.Addition can not get above-mentioned effect during less than 0.01 weight %, adds 1.1 weight % when above, not only uneconomical, and generate be difficult to molten admittedly once with the secondary double carbide, performance is produced adverse effect, so the interpolation scope is limited to 0.01-1.1 weight %.
Al:0.005-0.04 weight %
Al is strong de-acidying agent, is to make the very important element of product nucleus environment of solidified structure miniaturization with the REM reaction in molten steel.After considering formation product nucleus environment, residual A l and N combination are carried out the formation reaction of AlN, and the interpolation scope are limited to 0.005-0.04 weight %.
V:0.05-0.1 weight %, Nb:0.05-0.1 weight %
The bonding force of V and Nb and C is strong, can form fine carbide, makes the crystal grain miniaturization, improves toughness.If excessive interpolation, a large amount of VC, NbC, V2C that form as the one-time process carbide reduce toughness, so the addition of V and Nb is each defined in 0.05-0.1 weight % when solidifying.
N:0.0025-0.3 weight %
N is the important element of steel of the present invention, forms Nb (CN), ALN, TiN etc., and heat makes the crystal grain miniaturization when quenching, and suppresses the generation of MC type one-time process carbide when solidifying.In low-carbon (LC)/low alloy steel, generally cause toughness to reduce, cause low temperature brittleness, so by the following relational expression 3 that in further investigation of the present invention, obtains, basically the interpolation scope is limited to 0.0025-0.02 weight %, but consider steel of the present invention and when actual cold-peace pines for using,, obtain higher reinforcement matrix by the solution strengthening of nitrogen, improve the life-span, thereby be limited to below the 0.3 weight %.
[Al weight %]/[N weight %]=2: 1
REM (Y, Ce, La, Nd, Pr): 0.001-0.5 weight %
Adding rare earth element REM is in order to generate the RE class complex chemical compound of diameter below 5 microns in molten steel, with the control solidified structure, the cast structure that obtains perfecting, and be for the growth that suppresses crystal grain under the high temperature when the modified thermal treatment to improve shock-resistance.But, along with addition in the molten steel increases,, hinder above-mentioned effect on the contrary along with solubleness and concentration value with REM, Al, O, S increase, so be limited to relational expression 1, its scope is limited to 0.001-0.5 weight %.
Ca:0.0005-0.01 weight %
Ca is strong de-acidying agent, is the element that must add in the refining last process.Ca still controls the effective element of nonmetal inserting shape.Thermodynamics is considered the nonmetal inserting shape that control is added with REM, and addition is limited to 0.0005-0.01 weight %.
W+Co:0.01-05 weight %
W and Co are the elements of strengthening martensite matrix and improving hot strength and wearability.Because price is expensive, addition is limited to 0.01-0.5 weight %, and optionally adds for improving hot strength.
B:0.0001-0.005 weight %, Ti:0.001-0.1 weight %
B and Ti are to be optionally to add in order to improve hardenability more than 200 millimeters the time at materials used thickness and width.Relational expression according to the plain effect of boron (Boron Effect) in molten steel is limited to the addition of B in the 0.0001-0.005 weight % scope, and Ti is limited in the 0.001-0.1 weight % scope.
Shock-resistant, the snappiness of wearability of the present invention, the manufacture method of high-strength steel comprise following several steps:
Make the molten steel stage, molten steel contains V, the N of 0.0025-0.02 weight % of Al, 0.05-0.1 weight % of Mo, 0.005-0.04 weight % of Ni, 0.01-0.5 weight % of Cr, 0.01-0.1 weight % of Mn, 1.4-2.4 weight % of Si, 0.5-1.0 weight % of C, the 1.4-2.5 weight % of 0.26-0.48 weight %, remains to be Fe and unavoidable impurities;
Solidification stages is solidified above-mentioned molten steel under 1550 ± 80 ℃;
In the hot-work stage, above-mentioned solidification material is implemented hot-work down at 1100 ± 150 ℃;
Normalizing treatment and annealing stage are implemented normalizing treatment and annealing down at 650-1000 ℃;
In the quench treatment stage, implement quench treatment down at 800-1050 ℃;
In the tempering stage, implement tempering down at 80-700 ℃.
Can utilize composition 2, composition 3, composition 4 to replace above-mentioned molten steel here.
Above-mentioned quench treatment is in the stage, per 10 millimeters thickness carry out austenitizing more than 1 minute and solutionizing handle after, interim Cooling Control cooling (salt, oil, water, water+refrigerant) till cooling (salt, oil, water, water+refrigerant) or 180 ℃ continuously.
Above-mentioned temper after the per 10 millimeters thickness maintenance of the material in normal temperature to the 80 ℃ scope is more than 3 minutes, is carried out once above temper by air cooling or with the salt below 200 ℃, oil, water, water+refrigerant in the stage.
Embodiment
The chemical ingredients of the steel in the past of table 1 expression invention steel of the present invention and prior art.
Invention steel A, B, C, D, E, F mix fusion with pure iron and scrap iron in 60 tons of electric furnaces, handle through refining and vacuum outgas, the molten steel that obtains, and invention steel G, H, I, J, K, L, M, N, O, P, Q mix fusion with pure iron and scrap iron in 3 tons of electric furnaces, through refining, the molten steel that obtains.
Contain among invention steel B, C, G, L, M, the N: the Nb of N, the 0.01-0.1 weight % of V, the 0.0025-0.02 weight % of Al, the 0.05-0.1 weight % of Mo, the 0.005-0.04 weight % of Ni, the 0.01-0.4 weight % of Cr, the 0.01-0.05 weight % of the Si of the C of 0.26-0.36 weight %, 1.6-2.2 weight %, the Mn of 0.5-1.0 weight %, 1.4-2.4 weight %, the Ca of 0.0005-0.01 weight % remain and are Fe and unavoidable impurities.
Invention steel A and E add the B of 0.0001-0.005 weight % and the Ti of 0.001-0.1 weight % after making molten steel with mentioned component and compositing range again.
After invention steel D, E, J, K, O, P, Q make molten steel with mentioned component and compositing range, for obtaining containing the steel of rare earth element, add the rare earth element REM (Y, Ce, La, Nb, Pr) of 0.001-0.5 weight % again, rare earth element satisfies relational expression [REM weight % (Y, Ce, La, Nd, Pr)+Al weight %]/[S weight %]=2-90 and [Ca weight %]/[S weight %]=1, [REM (Y, Ce, La, Nd, Pr)+Al]/[O+S]=0.001 * 10 with the ratio of final S content
-5-30000 * 10
-5[weight %].
Invention steel F, H, I, K, P are to be further harden energy and the thermal property of improving, and form in the present invention to reach in the scope that satisfies composition 3 on, by improving the content of N, Mn, Cr, Ni, each composition of Mo, and add W and Co, and wherein the total content of W+Co is 0.01-0.1 weight %, thus the molten steel that makes.
Then, the molten steel of invention steel A, B, C, D, E, F is made 6 tons of steel ingots at 1550 ± 80 ℃, and the thermal stretch postcooling is to normal temperature, then again 1200 ± 50 ℃ carry out equal thermal treatment after, carry out hot calender or forging at 1100 ± 150 ℃, make 120 * 255 millimeters sheet material.In addition, the molten steel of invention steel G, H, I, J, K, L, M, N, O, P, Q is made 2.6 tons of steel ingots at 1550 ± 80 ℃, the thermal stretch postcooling is to normal temperature, then again 1200 ± 50 ℃ carry out equal thermal treatment after, carry out hot calender or forging at 1100 ± 150 ℃, make 60 * 255 millimeters sheet material.
Steel R, S, T, U, V, W, X had proper constituent separately in the past, used the same procedure with embodiment, must melt steel with 60 tons of Electric Cooker after, make 6 tons of steel ingots, and hot calender is made 120 * 255 millimeters sheet material.
Table 1
(weight %)
Invention steel A, B, C, D, E, F make product by two kinds of methods under hot state in hot calender.The first, the method identical with stress relief annealed method with the normalizing of comparative example; The second, after cooling is controlled to assigned temperature under the hot state of the very big feature of the embodiment of the present invention research and development, slowly cool off by rapid cooling and BOX, reduce temperature, make product.These all have mechanical cutting and the feasible hardness HB200-HB250 of mechanical workout under the commercialization state.Invention steel G, H, I, J, K, L, M, N, O, P, Q are by after the second method cooling control, slowly cool off by rapid cooling and BOX, make product.
Steel R, S, T, V, W were steel alloy in the past, and by common known normalizing and low-temperature annealing, and steel U and X were the alloy machined steel in the past, by annealing, gave machinability.
In addition, the modified thermal treatment of embodiment is meant quenching and tempering, quenching is after 800-1050 ℃ down per 10 millimeters thickness carry out 1 minute austenitizing and solid melt processed, continuously interim Cooling Control cooling (salt, oil, water, water+refrigerant) till cooling (salt, oil, water, water+refrigerant) or 180 ℃; Tempering be with the material in normal temperature to the 80 ℃ scope after 80-700 ℃ of down per 10 millimeters thickness keep more than 3 minutes, carry out once above temper by air cooling or the salt below 200 ℃, oil, water, water+refrigerant.
Fig. 1 represents in the modified thermal treatment to implement the micro organization's observations after 840 ℃ and 960 ℃ of quenchings and 180 ℃ and the 390 ℃ of tempering, and wherein micro organization is the carbon amount of invention steel among the representative embodiment and the micro organization of the invention steel B that other alloying element amounts are intermediate degree.
The tissue of as-quenched condition is the martensite that contains the 10% following retained austenite of having an appointment, and according to different quenching, has the different substrates tissue.Under 840 ℃, quenching structure has 10% ferrite, and hardness is HRC46, and behind low temperature and high tempering, ferrite does not change yet.Under 960 ℃, quenching structure is fine, is changed to martensite fully, and after 180 ℃ of tempering, tissue is changed to fine tempered martensite (tempered martensite), and after 390 ℃ of tempering, tissue is changed to fine troostite (troostite).
Therefore, in the present embodiment, be that below 10% 800 ℃ are the quenching temperature lower limit with the ferrite of performance tissue and mechanical characteristics, the most suitable quenching temperature of steel of the present invention is 860-1040 ℃.
Fig. 2 has compared invention steel B, F and steel R, X quenched the back in the Hardness Distribution of different tempering temperatures maintenances after 2 hours in the past.Invention steel B does not almost have hardness to reduce till the temperature to 400 ℃, and hardness reduces slightly till 500 ℃, and hardness reduces significantly in the time of more than 500 ℃.Compare with the X of steel in the past as the alloy machined steel, the situation of the two is identical till 400 ℃, but does not have the secondary hardening of steel X in the past, and the invention steel F that gives thermal property in time more than 500 ℃ has secondary hardening, expression HRC54.Compare with the R of steel in the past of steel alloy, tempering temperature is high more, and the amplitude that reduces of steel R hardness was big more in the past, and the alloying element amount was with the similar invention steel of steel R B was by the high silicon of feature of the present invention and the combination of alloying element in the past, and the hardness reduction can not increase.
Invention steel P has natural characteristics of the present invention, particularly be added with W, the Co, the N that improve hot properties, be used for hot purposes, expression is high tempering (tempering) resistance fully, compare with the X of steel in the past of hot-work steel, also under 600 ℃ of high temperature, have high tempering resistance.
Invention steel G has the natural characteristics of steel of the present invention based on the carbon that contains 0.46 weight % and the nitrogen of 0.14 weight %, guarantees that simultaneously quenching hardness is HRC62, has high quenching hardness, compares with the X of steel in the past as steel alloy, has good tempering resistance.
Shown in the table 2, represent the different quenching and tempering temperature of invention steel D of steel of the present invention and the impelling strength when implementing normalizing treatment and not implementing normalizing treatment.
Under modified heat-treat condition, impelling strength is confirmed as in micro organization's variation of invention steel to be changed, its result, the invention steel in the mechanical characteristics under the modified heat-treat condition in 840-980 ℃ of scope, quenching temperature is high more good more, notched bar impact strength does not have wide variation in the time of 1000 ℃, and notched bar impact strength sharply reduces in the time of 1050 ℃.
Invention steel quenching temperature is 840-1000 ℃, tempering temperature is respectively 180 ℃ and 400 ℃, notched bar impact strength is 4.5-7.5 kilogram force-meter/square centimeter at the state of implementing normalizing treatment with when not implementing the state of normalizing treatment, higher slightly when implementing normalizing treatment, but difference is little, has high impelling strength when 180 ℃ of low-temperaturetemperings.Therefore,, also have good impelling strength even steel of the present invention does not carry out low-temperaturetempering and normalizing treatment, and low cost of manufacture, so have superperformance.
Table 2
The steel of invention shown in the table 3 A, B, C, D, E, F and invention steel G, H, I, J, K, L, M, N, O, P, Q and steel R, S, T, U, V, W, X hardness, impact characteristics and the tensile properties after modifier treatment in the past.(invention steel A-invention steel Q → quenching: 960-1020 ℃, tempering: 180-600 ℃; Steel R, S → quenching in the past: 850 ℃, tempering: 180 ℃; Steel T, V, W → quenching in the past: 960 ℃, tempering: 180 ℃; Steel U, X → quenching in the past: 1050 ℃, tempering: 530 ℃)
In the table 3, be, compare with steel in the past, all invention steel all have the notched bar impact strength of 6 kilogram force-meters/more than the square centimeter when approximate hardness (HRC50-53), guarantee very good shock absorption energy, therefore can be used as the excellent material of shock-resistant parts, and can guarantee the tensile strength of 160-200 kilogram force/square millimeter.Steel of the present invention is compared with steel in the past, it is characterized in that not only having high tensile strength, and have very high impelling strength and a unit elongation, and the difference between tensile strength and the yield strength is compared littler with steel in the past, guarantee high-yield strength, is subjected to the very big external stress also can be damaged thus.
Table 3
Fig. 3 is with invention steel B and invention steel P and steel R and wearing character relatively behind the normal temperature check for wear of steel X in the past in the past.The invention steel and in the past the initial hardness of steel all be HRC53.In the result shown in the table 3, along with the wearing and tearing distance increases, invention steel and all increases gradually of abrasion loss of steel in the past, steel R increased since 15 meters abrasion losies in the past, sharply wear and tear during to 30 meters, and steel X sharply increased since 25 meters abrasion losies in the past, near invention steel capital abrasion loss 30 meters increases.The abrasion loss of invention steel is compared with steel in the past, changes minimum.
Therefore, under hardness much at one, the invention steel is compared with steel in the past, significantly reduces with the abrasion loss of distance.So the strong basis matter strengthening effect of invention steel by Si under the condition that has with the almost similar alloying element amount of steel in the past, still has very good wearability.
Fig. 4 be expression to invention steel D and invention steel Q and in the past the material of 180 millimeters of the diameters of steel R, V, X carry out the Hardness Distribution from the surface to the central part after the quench treatment.Among the figure, the hardness of invention steel slowly reduces from the surface to the central part, thus compare with steel R, V in the past, can guarantee good sclerosis can, in large diameter modified thermal treatment, also can guarantee good mechanical properties.
Fig. 5 a, b represent this material invention back as the most widely used scrap iron cutter blades of a kind of present steel of the present invention (Scrap Shear Blade), and Fig. 6 represents the stainless steel materials shear knife of another purposes of steel of the present invention.
When table 4 is mounted on the actual stapling machine scrap iron cut-out equipment, invention steel B, D, F, G, I, J, K, L, N, P, Q and the scrap iron cut-out amount of steel R, X in the past, the X of steel in the past with the most widely used present hot-work steel is a benchmark value 100%, compares the result who draws.
Shock-resistant, the wear-resistant high elastic and strength steel-foregoing invention steel of the most suitable alloy composition that meets high silicon was with steel R, X compared in the past, has longer work-ing life, particularly, with compare as the most of both at home and abroad X of steel in the past that uses of scrap iron cutter blades and shear knife parts, minimumly increase 25%, increase life-span of 125% at most.
In steel of the present invention, the invention steel D, G, J, L, N, the Q that are added with invention steel F, I, K, the P of the strong alloying element of thermotolerance and do not add above-mentioned alloying element compare, manufacturing cost is slightly higher, and is very big but the life-span of comparing with manufacturing cost prolongs.Therefore, at present the most frequently used when cutting off the hot-work steel-steel X compared in the past with carry out scrap iron under stringent condition, and manufacturing cost reduces among 50% the embodiment, obtain very high income, and mould life is also very long.
Fig. 7 represents to represent thermodynamics/thermal treatment numerical analysis figure of the invention steel K of steel of the present invention.Fig. 7 a is the Fe-C phasor (Vertical SectionThermo-Calc.Phase Diagram) that the present invention represents invention steel K when calcining vertical section, carbon content is 0.48 weight % when following in each target alloying element of steel of the present invention, can obtain tissue and precipitated phase that the present invention wishes.Fig. 7 b is the continuous cooling change curve (CCT) of foregoing invention steel K, and ferrite front end (Nose) moves to the side that keeps left, and is changed to the ferritic structure that does not produce bainite and martensite (causing the crack during air cooling).After steel of the present invention carried out thermoplasticity processing, do not need to carry out normalizing thermal treatment and annealing thermal treatment, can cut off and process, when carrying out oxygen blast and cutting off, can not cause the crack yet, obtain satisfactory prod.
Table 4
| Kind | Hardness (HRC) | Scrap iron cut-out amount | The life-span rate of rise |
| |
51 | 2,500 tons | 125％ |
| Invention steel D | 50.5 | 2,600 tons | 130％ |
| |
51 | 3,000 tons | 150％ |
| |
53 | 2,920 tons | 146％ |
| Invention steel I | 53 | 4,000 |
200％ |
| Invention steel J | 51.5 | 3,320 tons | 166％ |
| |
53 | 3,600 tons | 180％ |
| Invention steel L | 51.5 | 3,120 tons | 156％ |
| Invention steel N | 52 | 2,400 tons | 120％ |
| Invention steel P | 52 | 5,000 tons | 250％ |
| Invention steel Q | 52 | 2,700 tons | 135％ |
| Steel R in the past | 51 | 600 |
30％ |
| Steel X in the past | 51 | 2,000 |
100% (benchmark value) |
As mentioned above, shock-resistant, anti abrasive snappiness of the present invention, high-strength steel, though alloying element content is low, but the most suitable mixing by high content silicon and each alloying element, compare with steel in the past, weldability, low-temperaturetempering resistance and high tempering resistance, sclerosis energy, wearability (utilizing Si to strengthen matrix) and mechanical characteristicies such as impelling strength and tensile strength are very good, have high rigidity, high strength, high tenacity and snappiness, so be used for stringent condition mould life in following time and component life is longer than steel in the past far away.
Particularly, steel of the present invention suitably mixes the alloying element of low levels based on high silicon, and is applicable to by employing and the heat treating method of the intrinsic alloy composition of steel of the present invention obtains snappiness, high-strength steel.But steel relied on high alloy to improve characteristic in the past, and the manufacturing cost height can not oxygen blast directly cut off (because the crack takes place).Steel of the present invention is based on high silicon, the alloying element that suitably mixes low levels, so manufacturing cost reduces by 50%, but and oxygen blast cut off complicated shape (crack does not take place), reduce process cost, therefore low material price and low process cost can fully satisfy actual needs person's cost lowers the requirement.
Claims (6)
1, a kind of shock-resistant and anti abrasive high elastic and strength steel, wherein, described steel contains V, the N of 0.0025-0.3 weight % of Al, 0.05-0.1 weight % of Mo, 0.005-0.04 weight % of Ni, 0.01-1.1 weight % of Cr, 0.01-1.05 weight % of Mn, 1.4-3.4 weight % of Si, 0.5-1.5 weight % of C, the 1.4-2.5 weight % of 0.26-0.48 weight %, residue is Fe and unavoidable impurities
Described steel also satisfies following relation,
Si weight %/Mn weight %=2.6-3.2, and
Al weight %/N weight %=2: 1.
2, shock-resistant and anti abrasive high elastic and strength steel according to claim 1, wherein, in order to control solidified structure, described steel also contains the REM of 0.001-0.5 weight % and the Ca of 0.0005-0.01 weight %, and satisfies following relational expression:
The concentration formula:
(REM weight %+Al weight %)/S weight %=2-90,
Ca weight %/S weight %=1, and
The solubleness formula:
(REM+Al)/(O+S)=0.001 * 10
-5-30000 * 10
-5Weight %,
Wherein said REM represents rare earth element.
3, shock-resistant and anti abrasive high elastic and strength steel according to claim 2, wherein, described steel also contains a kind of among the Nb of W+Co, 0.01-0.1 weight % of Ti, 0.01-0.5 weight % of B, 0.001-0.1 weight % of 0.0001-0.005 weight %.
4, a kind of manufacture method of shock-resistant and anti abrasive high elastic and strength steel, wherein, this method comprises the steps:
Make the stage of the molten steel of the described composition of claim 1-3;
The stage that described molten steel is solidified under 1550 ± 80 ℃;
The material that the described stage of solidifying obtains is implemented the hot worked stage down at 1100 ± 150 ℃;
Implement normalizing treatment and annealed stage down at 650-1000 ℃;
800-1050 ℃ of stage of implementing quench treatment down;
Implement the temper stage down at 80-700 ℃.
5, the manufacture method of shock-resistant and anti abrasive high elastic and strength steel according to claim 4, wherein, in the stage of described quench treatment, per 10 millimeters thickness carry out austenitizing more than 1 minute and solutionizing handle after, interim Cooling Control cooling postcooling is to normal temperature till being quickly cooled to the continuous cooling of normal temperature or carrying out 180 ℃, and cooling is salt, oil, water or water+refrigerant with agent.
6, the manufacture method of shock-resistant and anti abrasive high elastic and strength steel according to claim 5, wherein, described temper is in the stage, with the material in normal temperature to the 80 ℃ scope after 80-700 ℃ of down per 10 millimeters thickness keep more than 3 minutes, carry out once above temper by air cooling or with the cooling below 200 ℃ with agent, cooling is salt, oil, water or water+refrigerant with agent.
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| KR1020040097064A KR100619841B1 (en) | 2004-11-24 | 2004-11-24 | High elasticity and high strength steel in the composition of high silicon with low alloy for the purpose of impact resistance and abrasion resistance and manufacturing method of the same steel |
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