CN101861407A - Martensite Stainless Steel, by the production method of its parts of making and the parts of producing thus - Google Patents
Martensite Stainless Steel, by the production method of its parts of making and the parts of producing thus Download PDFInfo
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- CN101861407A CN101861407A CN200880106281A CN200880106281A CN101861407A CN 101861407 A CN101861407 A CN 101861407A CN 200880106281 A CN200880106281 A CN 200880106281A CN 200880106281 A CN200880106281 A CN 200880106281A CN 101861407 A CN101861407 A CN 101861407A
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- 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
- C21D1/19—Hardening; Quenching with or without subsequent tempering by interrupted quenching
- C21D1/22—Martempering
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/002—Heat treatment of ferrous alloys containing Cr
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- 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
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Abstract
A kind of Martensite Stainless Steel, it is characterized in that, represent with weight percent, it comprises: 0.22%≤C≤0.32%0.05%≤N≤0.15%, and 0.33%≤C+N≤0.43%10%≤Cr≤12.4%0.10%≤V≤0.40%0.10%≤Mo≤1.0% trace≤Ni≤1.0% trace≤Mn≤1.0% trace≤Si≤1.0% trace≤W≤1.0% trace≤Co≤1.0% trace≤Cu≤1.0% trace≤Ti≤0.010% trace≤Nb≤0.050% trace≤Al≤0.050% trace≤S≤0.020% trace≤O≤0.0040% trace≤P≤0.03% trace≤B≤0.0050% trace≤Ca≤0.020% trace≤Se≤0.010% trace≤La≤0.040% trace≤Ce≤0.040% all the other be the impurity of introducing in iron and the production operation.The method of producing parts by such steel, and the parts that obtain in this way for example are used to produce the mould element of plastic material goods.
Description
Technical field
The present invention relates to steel-making, more specifically, relate to and be used for for example preparing the Martensite Stainless Steel of producing the mould of plastic material by injection moulding.
Background technology
In order to produce the mould that is used for the material injection moulding, industrial use chromium content is 12%～15% (weight percentage, all pointed content of this paper remainder also are weight percentage), silicone content less than 1%, manganese content less than 1%, carbon content be 0.16%～0.45% and since production operation and naturally the nitrogen content of introducing be generally AISI 420 family's stainless steels of 0.03% at the most.In general, the content of vanadium is no more than 0.1%, and is the simple interfused result of raw material.In the same manner, the content that contains molybdenum and be raw material interfused result and molybdenum is no more than 0.2%, unless add 0.2%～1.0% molybdenum in order to improve erosion resistance.More specifically, label is the steel of X40Cr14, because its carbon content is 0.36%～0.45% and can have hardness above 50HRC, thereby provides significant wear resistance.
Consider the purposes of anticipation, the validity that must come evaluating material by the good equilibrium that obtains between the following performance:
-ideal wear resistance can produce the parts of how much guaranteed maximum quantities of regularity, comprises the plastic material that has abradability by binding fiber or other enhancement additive; This wear resistance is provided by the high rigidity level;
-enough toughness is in case rupture in hot-work, assembling, disassembling section or use; For crisp especially steel, have been found that this performance and a last performance tradeoff, along with hardness increases, toughness reduces;
But-good polishability can easily obtain the surface finish quality, thereby produce the plastic material parts with smooth homogeneous surface outward appearance on die surface; This steel must keep this polishing condition as far as possible for a long time;
-enough erosion resistances are to prevent in the storage process and use of mould, to have and occur in the production process of plastic material of slight or medium chemical corrosivity that spot loses, gets rusty, the variation of polishing condition; The most active material, for example by salting out chlorion, need be from the steel or the alloy of other families.
After blank is worked into the approximate dimension of final form, make mould under in check atmosphere, in stove, pass through following heat treatment operation:
-quenching temperature is brought up to 1000～1050 ℃, be incubated tens of minutes then;
-to be quenched to temperature under gaseous tension be 80 ℃;
-elevated temperature carries out two tempering circulations.
Two temperature ranges of general proposition are carried out tempering:
-low-temperaturetempering: 150～250 ℃,
-in the tempering of second hardened zone of steel under 490/530 ℃.
In theory, in identical scope, carry out two successive tempering operations.
Must think over the accurate selection of processing parameter.
For quenching, on metallurgy, recommend to seek high annealing temperature, to obtain favourable martensitic microstructure.But high annealing temperature is impelled distortion and is produced unrelieved stress, and this unrelieved stress can cause cracking, and in practice, gaseous tension is defined as 2～4 crust.
When quenching stops, before proceeding tempering operation,, then might ftractureing if cooling is proceeded up to room temperature.But, be chosen in about 80 ℃ usually and stop the refrigerative way and have the risk remain with residual austenite, particularly be fixed under the situation below 500 ℃ at subsequently tempering operation all the more so, the therefore nominal hardness that can not obtain to wish.
For tempering operation, select low temperature only to allow partly to overcome restriction, and if the composition of steel and the circulation of quenching made and retained residual austenite that and tempering operation can not decompose described residual austenite, then the hardness that can not obtain to wish.The high tempering operation is decomposed austenite and is discharged unrelieved stress, but reduces intensity and erosion resistance.
The cost problem that also has these steel, because they need high alloying element content, and alloying element content should reduce and do not damage the performance of hope.
Summary of the invention
The objective of the invention is to determine a kind of steel compositions of economy, it is used to comprise the purposes such as mould of producing at plastics that for reference substance AISI 420 and X40Cr14, it has following characteristic:
-under the state after the processing, preferential equivalent hardness is 49～55HRC, with wear-resistant;
-suitable erosion resistance;
-the intensity of improvement under same rigidity;
But the polishing performance of-improvement;
-and in the industrial heat treatment process suitable, have these performances with conventional conditions.
For this reason, the present invention relates to a kind of Martensite Stainless Steel, it is characterized in that comprising (representing) with weight percent:
-0.22％≤C≤0.32％
-0.05%≤N≤0.15%, and 0.33%≤C+N≤0.43%
-10％≤Cr≤12.4％
-0.10％≤V≤0.40％
-0.10％≤Mo≤1.0％
-trace≤Ni≤1.0%
-trace≤Mn≤1.0%
-trace≤Si≤1.0%
-trace≤W≤1.0%
-trace≤Co≤1.0%
-trace≤Cu≤1.0%
-trace≤Ti≤0.010%
-trace≤Nb≤0.050%
-trace≤Al≤0.050%
-trace≤S≤0.020%
-trace≤O≤0.0040%
-trace≤P≤0.03%
-trace≤B≤0.0050%
-trace≤Ca≤0.020%
-trace≤Se≤0.010%
-trace≤La≤0.040%
-trace≤Ce≤0.040%
All the other are iron and the impurity introduced owing to production operation.
Be preferably 0.08%≤N≤0.12%.
Be preferably 11.0%≤Cr≤12.4%.
Be preferably 0.15%≤V≤0.35%.
Be preferably trace≤Si≤0.5%.
Be preferably 0.10%≤Mo+W/2≤1.20%.
Be preferably trace≤Ti≤0.003%.
Be preferably trace≤Nb≤0.010%.
Be preferably trace≤O≤0.0015%.
Be preferably trace≤S≤0.003%.
Be preferably trace≤Mn+Cu+Co≤1.8%.
The invention still further relates to a kind of method that is used to produce the Martensite Stainless Steel parts, it is characterized in that:
The steel of-production, casting, forging or rolling the above-mentioned type and annealing;
The described steel of-processing is to give the shape of described parts to it;
-under 990～1040 ℃, preferred 1000～1030 ℃ temperature with the steel austenitizing of being processed;
-speed with 10～40 ℃/minute under 800～400 ℃ temperature of the steel behind the austenitizing is quenched;
-steel after quenching is carried out the double tempering operation, to give its final hardness.
Described tempering operation can carry out minimum 2 hours at every turn under 200～400 ℃, preferred 300～380 ℃ temperature, and guarantees to keep this nominal temperature at least 1 hour in core, to obtain the hardness of 49～55HRC.
Described tempering operation can carry out under 530～560 ℃ temperature minimum 2 hours at every turn, and guaranteed to keep this nominal temperature at least 1 hour in core, to obtain the hardness of 42～50HRC.
The invention still further relates to a kind of Martensite Stainless Steel parts, it is characterized in that the element that production uses this method to produce according to preceding method.
This can be the mould element that is used to produce the plastic material goods.
Be to be understood that, the present invention is based on a kind of steel compositions, the content of its carbon and chromium is positioned at the lower limit of the scope of general requirement simultaneously, even chromium content is lower than the scope of general requirement sometimes, and makes other elements existence or that must limit or avoid meet accurate condition.Production method is relevant with said composition.
The inventor mainly considers performance described steel, that follow production operation, particularly follows the performance of above-mentioned industrial treatment, rather than meets the performance of the steel of laboratory condition.For the work of optimizing alloying element in order to limit its introducing amount, study.
It is as follows to cause producing principal element of the present invention.
But the polishing performance of described steel and the surface quality under the polishing condition are owing to following factor reduces:
-there is a nonmetal oxide inclusion, this inclusion is reflected light and further decompose when contacting with abrasive material or expose not, and forms remaining striped or " comet tail " at die surface;
-dendritic segregation, it forms and produces harder zone or line naturally on die surface in the solidification process of rod, described harder zone or line and softer zone or line alternately because soft zone is regional recessed faster than hard, so in polishing process, produce ripple;
-exist in undissolved micro-chromium carbide in the hardening step.
In general, for the steel of this family, intensity is medium, and for given hardness, along with chromium content increases, intensity reduces.Its by equilibrium composition, particularly add nickel and manganese and can be improved, nickel and manganese allow to keep remaining austenite in hardening step.If tempering operation is carrying out more than 500 ℃, this scheme no longer includes effect, has been found that this scheme is unstable and harmful to the generation of hardness.No longer kept this scheme, particularly because this scheme is incompatible with hope minimizing alloying element content.
Target in order to realize determining determines:
-on the one hand, produce described steel according to the currently known methods that the non-metallic inclusion that limits oxidation exists, thereby make described steel have low O content,
-on the other hand, reduce alloying element comprehensively, introduce nitrogen and optimize balance between the element, thus improve intensity, reduce dendritic segregation and limit the density of microprecipitation thing.
Description of drawings
The present invention may be better understood from the following description that provides with reference to the following drawings:
-Fig. 1 illustrates reference steel and according to the microtexture of the sample of two kinds of steel of the present invention, shows the density and the distribution of micro-carbide under the state that uses these steel;
The temperature that-Fig. 2 illustrates two kinds of tempering operations is to the influence according to the erosion resistance of steel of the present invention;
-Fig. 3 illustrates the influence of the temperature of tempering operation to erosion resistance;
-Fig. 4 illustrates the interaction to erosion resistance of the content of Cr and quenching velocity;
-Fig. 5 illustrates according to steel of the present invention with according to the hardness of the reference steel of tempering operation temperature.
Embodiment
Table 1 is listed the composition of the sample of being studied.Sample " reference substance " is equivalent to the steel of traditional type X40Cr14.Sample embodiment 1～embodiment 7 is not according to the present invention, but allows to overcome the shortcoming that does not meet all conditions of the presently claimed invention and relate to.Sample Inv.1 and Inv.2 are according to of the present invention.
So, an object of the present invention is to provide a kind of steel of optimization, its scope according to industrial quench rates is handled, preferably, under low temperature (＜400 ℃), carry out the double tempering operation subsequently, make that hardness is 52HRC, and in its conventional application, intensity and erosion resistance are equal to or greater than intensity and the erosion resistance of reference steel AISI 420 or X40Cr14.
In addition, an object of the present invention is add-on at possible extent upper limit alloyage element, the add-on of metallic element particularly, to reduce production cost, prevent the degree that there is residual austenite behind the hardening step and reduces dendritic segregation, dendritic segregation is deleterious to intensity and quality of finish.
For this reason, the inventor has obtained qualification relevant result following and to the composition of steel of the present invention.
Nitrogen content must be preferably 0.08%～0.12% between 0.05% and 0.15%.This element exists with high-content ground systematicness because it be for form V (C, N) type carbonitride institute is requisite, after the chromium carbide dissolving, this carbonitride can prevent the grain growth in the austenitization.But if above the solubility limit in solid-state, then excessive content is deleterious, and will cause the metallographic defective.The combination of nitrogen and carbon is to give hardness and nitrogen relates to erosion resistance.The content of nitrogen can be regulated by be blown into the GN 2 when producing the liquid steel.
The main contribution of carbon is to give needed hardness with nitrogen.Consider needed hardness after low-temperaturetempering, its per-cent is necessary for 0.22%～0.32%.In addition, for the hardness that obtains to wish after tempering, total C+N is necessary for 0.33%～0.43%.
Chromium is given the steel erosion resistance.Consider used industrial quench rates and selected tempering range, and according to mechanism set forth above, its content is necessary for 10%～12.4%, is preferably 11.0%～12.4%.
Content of vanadium is necessary for 0.10%～0.40%, is preferably 0.15%～0.35%.The existence of vanadium is absolutely necessary for micron throw out and the nanometer throw out with carbon and nitrogen formation sufficient density, and described throw out can prevent grain growth.Excessive content can be deleterious, because carbon is excessive fixing unfavorable to intensity and polishing condition quality to the formation harmful and carbide discrete or the cluster form in solidification process of hardening.
Molybdenum replenishes the effect of chromium aspect erosion resistance.The existence of molybdenum is owing to reclaimer operation, or deliberately add, it is measured between 0.10%～1.0%.Bigger content can be deleterious, and this is because this increases the degree of dendritic segregation and has the risk that forms delta ferrite.
Nickel can exist with the content less than 1.0%, particularly is mingled with by raw material.Do not find in this scope, to add nickel toughness is had beneficial effect.But bigger content can keep residual austenite under the state after the processing.
Because production method and useful raw materials, manganese are the elements that exists naturally in this family's steel.Find to have beneficial effect, and found must be with its concentration limit to 1.0%, to prevent the residual austenite after the thermal treatment.
Silicon is because the production of steel and deoxidation and existence naturally.Its content has to be limited to 1.0%, is preferably 0.5%, because silicon acts on solidification process and δ/γ changes, therefore, owing to there was this phase before forging beginning when solidifying end, may cause existing delta ferrite or spot segregation effect.
Tungsten can be less than 1.0% content exists to product without any useful or deleterious effects.But, since its oneself effect or with the synergy of molybdenum, tungsten can promote to exist localized precipitation or the segregation that delta ferrite or any stage in hot mechanical process cause owing to the existence of delta ferrite under user mode.Preferably eligible 0.10%≤Mo+W/2≤1.20%.
Cobalt and copper are not found useful effect, but can exist to be less than or equal to 1.0% content; Higher content may promote the existence of residual austenite.
Preferably there is the risk of residual austenite in the summation of the content of Mn, Cu and Co less than 1.8% with restriction.
Titanium and niobium are to form stone sedimentary very active element, and described throw out is harmful to the quality of polishing condition.It is low as far as possible that its concentration must keep: for Ti, be 0.010% to the maximum, be preferably maximum 0.003%, for Nb, be 0.050% to the maximum, be preferably maximum 0.010%.
The aluminium that adds for the deoxidation of steel may keep existing with the form of oxide inclusion, and oxide inclusion is very deleterious to polishing condition.Addition must adapt to used production method.Maximum level is 0.050% can tolerate that condition is that it does not cause existing in a large number aluminum oxide or pure aluminium silicate inclusion, exists aluminum oxide or pure aluminium silicate inclusion can cause O to surpass acceptable content (0.0040%, be preferably 0.0015%) in a large number.
For preventing to form the sulphur inclusion, sulphur content is preferably and is restricted to less than 0.003%.Yet, in order to improve the infringement to a certain extent of processing characteristics and polishing condition quality, also can with promote that (Se mostly is 0.010% most for another kind of element that spherical sulfide forms; Ca mostly is 0.020% most; La mostly is 0.040% most; Ce mostly is 0.040% most) together, in 0.003～0.020% scope, initiatively add.
The maximum level of oxygen is 0.0040%, is preferably 0.0015%.This element is the indicator of inclusion density, and the polishing condition to the surface when inclusion density is too high is harmful.It is low as far as possible that this content must keep, result, the necessary production method of selecting steel.In practice, known method allows to be low to moderate the value of O=5ppm economically under the acceptable condition.
The content of phosphorus is restricted to 0.03%, and this is the common content in this class steel.In this scope, do not find the deleterious effect of P.
In order to improve the quenching performance, can add boron, its content is no more than 0.0050%.
The preferred content of pointing out at some elements can utilize separately, and not necessarily with pointed other preferred contents combinations.
The element of not enumerating can exist with the content of producing the impurity level that is caused, and it can not change the present invention with the performance of optimizing.
For being used for plastics molding applications and purpose for limiting inclusion content and segregation to obtain the high-quality especially steel of high quality polished state, described product must be according to the regulation production of prior art.After fusing, described production must be included in deoxidation and the step of eliminating inclusion in the metallurgical reaction.Preferably, particularly for producing big mould and in order to obtain the polishing condition of extra best best, to carry out under slag using the melting operation again of consumable electrode, with improve inclusion purity and in whole quality with uniform mode distribute alloying element, particularly nitrogen.
In order to replenish the homogeneity and the tight type of microtexture, must utilize forging or rolling polishing and annealing operation to carry out hot mechanical transition subsequently.
After component processing is arrived net shape and before operation, according to preferred working method, described product must pass through heat treatment operation, this heat treatment operation is included in about 1020 ℃ (990～1040 ℃, be preferably 1000-1030 ℃) austenitizing, the hardening step of control, for example under neutral gas pressure, according to part dimension under 10～40 ℃/minute speed, at 200～400 ℃, be preferably the double tempering operation under 300～380 ℃ the temperature, to obtain the hardness of about 52HRC ± 2HRC, be generally 49～55HRC.
Randomly, for need not be,, can utilize at 530 ℃～560 ℃ double tempering by the steel that the present invention limited and to handle for being less than or equal to 50HRC and more than or equal to the hardness of 42HRC greater than the purposes of the hardness of 50HRC, under this condition, find that erosion resistance is enough.
For reference steel, the chromium carbide (M that exists with dispersion state
23C
6) dissolve in the austenitization before hardening step, and keep temperature to 1020/1030 ℃, to prevent grain growing.But, under this solvent temperature, keep the carbide of the significant quantity that distributes in even mode.By replace about 0.10%～0.15% carbon content with nitrogen, chromium content reduces about 2% and introduce vanadium simultaneously, observe under suitable quenching temperature that (C, nanometer throw out fixed crystal grain N) do not grow and the dissolving of most of chromium carbide by carbon vanadium nitride V.
For three kinds of compositions being studied, the equilibrated that uses (metallargist uses always) software THERMOCALC to utilize thermodynamics to simulate at 1030 ℃ compares the clear this variation (seeing Table 2) of reckoner.
Reference substance form with composition of the present invention between, observed on Industrial products, as to be illustrated in micron carbide among Fig. 1 effective density obviously, reduce effectively, this quality for polishing condition is a favourable factor.
For reference steel, according to rudimentary knowledge, in theory, corrosion resistant ability is mainly relevant with the chromium content that can obtain in the matrix, and calculation of thermodynamics shows that undissolved carbide has been fixed about 0.9% chromium in austenitization.For the experiment rank of coming alloy with vanadium and nitrogen, this quantitative change that is not used in corrosion resistant chromium must be lower than 0.1%.According to following formula:
P.R.E. (equivalent of anti-the spot corrosion)=%Cr+3.3 * %Mn+30 * %N
It allows according to the pitting corrosion resistance of each composition described composition to be classified usually, and is applied to effective composition of matrix.Find that according to table 2 Inv 1 is formed in experiment and Inv 2 has the coefficient approaching with reference substance.
Except considering that as above it also is favourable measuring with the significant condition of metal in operational phase the potentiality of thick as-quenched condition.The electrochemical method that carries out with standard A STM G 108 relates to the H in 1% weight
2SO
4In the aqueous solution, under the current potential of-550mV/ECS with sample polarization 15 minutes, the scan operation before and after carrying out with 60mV/min from-550mV to+550mV then.Characteristic curve intensity/current potential when returning can have two peaks, and one (peak 1) is the dissolving owing to matrix, and second (peak 2) is at higher current potential place, and be relevant with the dissolving in the chromium carbide throw out zone.Along with dissolution current becomes stronger, it is more responsive to corrosion that described steel becomes.In Fig. 2 and 3, characteristic curve has been shown.
According to current practice, when obtaining the hope hardness of about 52HRC, find heat treated two parameters, be that tempering temperature and quench rates are influential to erosion resistance about reference steel.
These have acted on chamber test shows by experiment:
A)
Drawing effect
Illustrate as Fig. 2, for the INV1 of casting, because the tempering operation that carries out in about 500 ℃ hardened zone, described steel becomes more responsive to corrosion.If erosion resistance is necessary top-priority characteristic for predetermined purposes, then low-temperaturetempering is operated thereby is preferred (200～380 ℃).
About all compositions of being tested, confirmed this trend, as shown in Figure 3.This shows at 380 ℃ or in the influence of operating near 500 ℃ 2 hours double tempering erosion resistance, this considers the corrosion current at 2 places, peak of Fig. 2.The accurate temperature of about 500 ℃ double tempering operation is regulated, making can be as obtain identical hardness after 380 ℃ double tempering operation.Have been found that particularly sample according to the present invention has and the closely similar erosion resistance of reference sample of operating at 380 ℃ of double temperings.
About low tempering temperature, confirmed that further erosion resistance reduces slightly at 200 ℃～380 ℃, reducing fast more than 400 ℃.
In order to make tempering operation have predetermined effect, must continue at least 2 hours, and its nominal temperature must keep 1 hour at least at parts core place.
B)
The effect of quenching velocity
Unexpectedly, as shown in Figure 4, Fig. 4 has compared two kinds of only experiment foundry goods of differing from one another of chromium content, and under the industrial condition of about 20 ℃/minute speed of cooling, the increase of this constituent content does not improve erosion resistance in 900/400 ℃ of scope.Low rate of cooling causes occurring peak 2, and peak 2 is represented the precipitation of carbide or nitride and become bigger along with chromium content increases its degree, and amplifies the corrosion current (peak 2) of matrix.
About the various compositions of being studied, verified these results.
According to the present invention, select compatible and 10～40 ℃/minute quenching velocity in 800 to 400 ℃ temperature range with the technical knowledge of heat treatment operation.
In a word, under the situation of industrial hardening step, obtained best erosion resistance, and in this configuration, the variation of chromium content in 10.5～15% scopes do not confirm the common beneficial effect of recognizing about this alloying element with the low-temperaturetempering operation.
Find that the reduction of quench rates and the raising of tempering temperature have identical disadvantageous effect to toughness.In the stretching and impact bending energy test process of the unnotched rod that is of a size of 55mmx10mmx7mm, this character is usually reduced by the stretching mechanic characteristic of routine and area simply and obtains.For related test, all samples are carried out 16 ℃/minute hardening step, carry out 2 hours double tempering operation then.The result who lists in the table 3 shows:
-for for example forming Inv.2, there is the unfavorable effect that reduces quench rates;
-in the katalysis of about 500 ℃ double tempering operation;
-for double tempering operation at low temperature (380 ℃), with respect to the reference sample, the hardness of two kinds of steel of the present invention/toughness isostatic excellent properties.
Composition permission of the present invention is quenched under industrial condition and obtain 52HRC or above hardness behind 380 ℃ of double tempering, still for the steel of this family of being made by rough quenched materials, takes place to soften in this scope, as shown in Figure 5.
Claims (16)
1. a Martensite Stainless Steel is characterized in that, represent with weight percent, it comprises:
-0.22％≤C≤0.32％
-0.05%≤N≤0.15%, and 0.33%≤C+N≤0.43%
-10％≤Cr≤12.4％
-0.10％≤V≤0.40％
-0.10％≤Mo≤1.0％
-trace≤Ni≤1.0%
-trace≤Mn≤1.0%
-trace≤Si≤1.0%
-trace≤W≤1.0%
-trace≤Co≤1.0%
-trace≤Cu≤1.0%
-trace≤Ti≤0.010%
-trace≤Nb≤0.050%
-trace≤Al≤0.050%
-trace≤S≤0.020%
-trace≤O≤0.0040%
-trace≤P≤0.03%
-trace≤B≤0.0050%
-trace≤Ca≤0.020%
-trace≤Se≤0.010%
-trace≤La≤0.040%
-trace≤Ce≤0.040%
All the other are the impurity of introducing in iron and the production operation.
2. steel according to claim 1 is characterized in that, 0.08%≤N≤0.12%.
3. steel according to claim 1 and 2 is characterized in that, 11.0%≤Cr≤12.4%.
4. according to each described steel in the claim 1～3, it is characterized in that 0.15%≤V≤0.35%.
5. according to each described steel in the claim 1～4, it is characterized in that trace≤Si≤0.5%.
6. according to each described steel in the claim 1～5, it is characterized in that 0.10%≤Mo+W/2≤1.20%.
7. according to each described steel in the claim 1～6, it is characterized in that trace≤Ti≤0.003%.
8. according to each described steel in the claim 1～7, it is characterized in that trace≤Nb≤0.010%.
9. according to each described steel in the claim 1～8, it is characterized in that trace≤O≤0.0015%.
10. according to each described steel in the claim 1～9, it is characterized in that trace≤S≤0.003%.
11., it is characterized in that trace≤Mn+Cu+Co≤1.8% according to each described steel in the claim 1～10.
12. a method of producing the Martensite Stainless Steel parts is characterized in that:
-production, casting, forging or rolling according to each described steel in the claim 1～11 and annealing;
The described steel of-processing is with the shape to described steel member of imparting;
-steel austenitizing under 990～1040 ℃, preferred 1000～1030 ℃ temperature after will processing;
-steel speed with 10～40 ℃/minute in 800～400 ℃ temperature range of austenitizing is quenched;
-steel after quenching is carried out the double tempering operation, to give its final hardness.
13. method according to claim 12, it is characterized in that, described tempering operation is each all to carry out minimum 2 hours under 200～400 ℃, preferred 300～380 ℃ temperature, and guarantees to keep nominal temperature at least 1 hour in core, to obtain the hardness of 49～55HRC.
14. method according to claim 12 is characterized in that, described tempering operation all carried out 2 hours under 530～560 ℃ temperature at least at every turn, and guaranteed to keep nominal temperature at least 1 hour in core, to obtain the hardness of 42～50HRC.
15. Martensite Stainless Steel parts is characterized in that, use the element of this method production according to each production in the claim 12～14.
16. parts according to claim 15 is characterized in that, it is a kind of mould element that is used to produce the plastic material goods.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| FR0757451A FR2920784B1 (en) | 2007-09-10 | 2007-09-10 | MARTENSITIC STAINLESS STEEL, PROCESS FOR MANUFACTURING WORKPIECES PRODUCED IN THIS STEEL AND PARTS PRODUCED THEREBY |
| FR0757451 | 2007-09-10 | ||
| PCT/FR2008/051525 WO2009034282A1 (en) | 2007-09-10 | 2008-08-25 | Martensitic stainless steel, method for making parts from said steel and parts thus made |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN101861407A true CN101861407A (en) | 2010-10-13 |
Family
ID=39272694
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200880106281A Pending CN101861407A (en) | 2007-09-10 | 2008-08-25 | Martensite Stainless Steel, by the production method of its parts of making and the parts of producing thus |
Country Status (9)
| Country | Link |
|---|---|
| US (1) | US20100276038A1 (en) |
| EP (1) | EP2188402B1 (en) |
| JP (1) | JP2010539325A (en) |
| KR (1) | KR20100059965A (en) |
| CN (1) | CN101861407A (en) |
| CA (1) | CA2698889A1 (en) |
| FR (1) | FR2920784B1 (en) |
| RU (1) | RU2010114173A (en) |
| WO (1) | WO2009034282A1 (en) |
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-
2007
- 2007-09-10 FR FR0757451A patent/FR2920784B1/en not_active Expired - Fee Related
-
2008
- 2008-08-25 US US12/677,464 patent/US20100276038A1/en not_active Abandoned
- 2008-08-25 KR KR1020107007729A patent/KR20100059965A/en not_active Application Discontinuation
- 2008-08-25 CA CA2698889A patent/CA2698889A1/en not_active Abandoned
- 2008-08-25 WO PCT/FR2008/051525 patent/WO2009034282A1/en active Application Filing
- 2008-08-25 CN CN200880106281A patent/CN101861407A/en active Pending
- 2008-08-25 EP EP08830336A patent/EP2188402B1/en not_active Revoked
- 2008-08-25 JP JP2010523562A patent/JP2010539325A/en active Pending
- 2008-08-25 RU RU2010114173/02A patent/RU2010114173A/en unknown
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Also Published As
| Publication number | Publication date |
|---|---|
| US20100276038A1 (en) | 2010-11-04 |
| EP2188402B1 (en) | 2012-05-23 |
| FR2920784A1 (en) | 2009-03-13 |
| KR20100059965A (en) | 2010-06-04 |
| JP2010539325A (en) | 2010-12-16 |
| WO2009034282A1 (en) | 2009-03-19 |
| CA2698889A1 (en) | 2009-03-19 |
| FR2920784B1 (en) | 2010-12-10 |
| RU2010114173A (en) | 2011-10-20 |
| EP2188402A1 (en) | 2010-05-26 |
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