Patent Application
20250003023
For the manufacturing of recent Body in White structures in the automotive industry, the press hardening process, also called the hot stamping or the hot press forming process, is a fast growing technology for the production of steel parts with high mechanical strength, which makes it possible to achieve weight reduction together with high resistance in case of vehicles collisions.
The implementation of press hardening using aluminized precoated sheets or blanks is known in particular from the publications FR2780984 and WO2008053273: a heat treatable aluminized steel sheet is cut to obtain a blank, heated in a furnace and rapidly transferred into a press, hot formed and cooled in the press dies. During the heating in the furnace, the aluminum precoating is alloyed with the steel of the substrate, thus forming a compound ensuring the protection of the steel surface against decarburization and scale formation. The heating is performed at a temperature which makes it possible to obtain partial or total transformation of the steel substrate into austenite. The austenite transforms during the cooling resulting from the heat extraction from the press dies, into microstructural constituents such as martensite and/or bainite, thus achieving structural hardening of the steel. High hardness and mechanical strength are thereafter obtained after press hardening.
In a typical industrial process, a pre-coated aluminized steel blank is heated in a furnace for a total duration of 3-10 minutes up to a temperature of 880-930° C. in order to obtain a full austenitic microstructure in the substrate and thereafter transferred rapidly into a forming press. It is immediately hot-formed into the desired part shape and simultaneously hardened by die quenching. With a 22MnB5 steel composition, the cooling rate must be higher than 50° C./s if full martensitic structure is desired even in the deformed zones of the part. Starting from an initial tensile strength of about 500 MPa, the final press hardened part has a fully martensitic microstructure and an Ultimate Tensile Strength value of about 1500 MPa.
For sake of productivity, it is desired to reduce as much as possible the heating duration of the pre-coated aluminized blank. For shortening this duration, WO2009095427 proposes to perform a first incomplete alloying of the aluminized blank, before a second heating and press hardening. In the first step, incomplete alloying takes place, the aluminum precoating is alloyed over at least 50% of its thickness with Fe. This first incomplete alloying step is achieved in practice through batch annealing for a few hours in a temperature range of 500° C. up to Ac1 (this temperature designating when austenite appears on heating) or through continuous annealing at 950° C. for 6 minutes. After this first step, the sheet is heated to a temperature higher than Ac1 and press hardened.
WO2010005121 discloses performing a first heat treatment of aluminized steel sheets through batch annealing in the range of 600-750° C. for a duration comprised between 1 hour and 200 hours. After this first step, the sheet is heated to a temperature higher than 700° C. and hot stamped.
WO2017111525 discloses also a first heat treatment in order to lower the risk of aluminum melting in the furnaces and to lower the hydrogen content. This first treatment is performed in the range of 450-700° C., for a duration comprised between 1 and 100 h. After this first heat treatment, the sheet is heated and hot-press formed.
However, the annealing treatments mentioned above have the following drawbacks or insufficiencies:
It is also desirable to have a manufacturing process wherein:
The present invention provides a process for manufacturing a non-stamped prealloyed steel coil, sheet or blank, comprising the following successive steps:
According to another process embodiment, the non-stamped prealloyed steel coil, sheet or blank comprises an alumina-containing oxide layer atop with a thickness higher than 0.10 μm.
Preferably, Vr1 is selected so that the sum of the area fractions of bainite and martensite is less than 30% in the steel substrate, after said cooling Vr1 and before subsequent heating.
Also preferably, Vr1 is selected so as to obtain a ferrite-pearlite structure in the steel substrate after said cooling Vr1 and before subsequent heating.
In another process embodiment, the temperature θ2 is higher than or equal to 100° C. and lower than 300° C.
The temperature θ2 is preferably higher than or equal to 300° C. and lower than or equal to 400° C.
In another preferred embodiment, θ2 is higher than 400° C. and less than or equal to 500° C.
The duration t2 is preferably comprised between 4 and 15 minutes.
In a particular embodiment, θi is equal to room temperature and the non-stamped coil sheet or blank, after cooling at room temperature, is heated up to temperature θ2.
In another particular embodiment, θi is equal to temperature θ2.
In another embodiment, immediately after maintaining the non-stamped coil, steel sheet or blank at a temperature θ2 comprised between 100 and 500° C. for a duration t2, the non-stamped steel coil, sheet or blank is cooled down to room temperature.
The invention relates also to a non-stamped prealloyed steel coil, sheet or blank, comprising a heat-treatable steel substrate covered by an alloyed precoating containing aluminum and iron, aluminum not being present as free aluminum, wherein the non-stamped prealloyed steel coil, sheet or blank contains an interdiffusion layer at the interface between the steel substrate and the precoating, with a thickness comprised between 2 and 16 micrometers, the interdiffusion layer being a layer with an α(Fe) ferritic structure, having Al and Si in solid solution.
According to an embodiment, the non-stamped prealloyed steel coil, sheet or blank comprises an alumina-containing oxide layer atop the alloyed precoating, with a thickness higher than 0.10 μm.
According to another embodiment, the diffusible hydrogen is less than 0.35 ppm.
The thickness of the non-stamped prealloyed steel coil, sheet or blank is preferably comprised between 0.5 and 5 mm.
In another embodiment, the steel substrate of the non-stamped prealloyed steel coil, sheet or blank has a non-uniform thickness.
Preferably, the sum of the area fractions of bainite and martensite is less than 30% in the steel microstructure.
Also preferably, the steel substrate of the non-stamped prealloyed steel coil, sheet or blank has a ferrite-pearlite microstructure.
The invention relates also to a process for manufacturing a press hardened coated steel part, wherein:
In a particular process embodiment, the non-stamped prealloyed steel blank manufactured according to any one of the process embodiments above is provided, the non-stamped prealloyed steel blank being not cooled at room temperature between maintaining at the temperature θ2 and heating at the temperature θ3.
In another process embodiment, the difference ΔHdiff between the content of diffusible hydrogen in the press hardened coated part and the content of diffusible hydrogen in the non-stamped prealloyed blank, is less than 0.10 ppm.
Preferably, the heating of the non-stamped prealloyed steel blank up to temperature θ3 is performed by a method selected among induction heating, resistance heating or conduction heating.
According to another preferred process embodiment, the microstructure of the steel substrate of the press hardened coated part comprises more than 80% of martensite.
In another process embodiment, the press hardened coated part has a yield stress higher than 1000 MPa.
The invention relates also to the use of a press hardened part manufactured according to any one of the embodiments above, for the fabrication of structural or safety parts of vehicles.
The invention will now be described in details and illustrated by examples without introducing limitations, with reference to the appended figures among which:
A steel sheet coil, or blank is provided, with a thickness ranging from 0.5 to 5mm. In a preferred range, the thickness is comprised between 0.5 and 2.5 mm. Depending on its thickness, it can be produced by hot rolling or hot rolling followed by cold rolling. Below 0.5 mm thick, it is difficult to manufacture press hardened parts fulfilling the stringent flatness requirements. Above a sheet thickness of 5 mm, thermal gradients across the thickness can occur during heating or cooling steps, which can cause microstructural, mechanical or geometrical heterogeneities.
This initial product can be under the form of coil, which is itself obtained from coiling of a rolled strip. It can be also under the form of strip, obtained for example after uncoiling and cutting a coil. Alternatively, it can be under the form of a blank, obtained for example from blanking or trimming of unwound coils or strips, the contour shape of this blank being more or less complex in relationship with the geometry of the final press hardened part.
The initial product can have a uniform thickness. It can have also a non-uniform thickness within the range mentioned above. In the latter case, it can be obtained by processes known by themselves, such as tailored welding of blanks or tailored rolling. Thus, tailored welded blanks resulting from the welding of sheets having different thicknesses, or tailored rolled blanks, can be implemented.
The coil, sheet or blank is composed of a flat steel substrate precoated with aluminum, or with aluminum-based alloy, or with aluminum alloy. Thus, at his stage, this flat steel substrate, under the form of coil, sheet, or blank, has not been submitted to any stamping operation in view of obtaining the final part geometry.
The steel of the substrate is a heat treatable steel, i.e. a steel having a composition which makes it possible to obtain martensite and/or bainite after heating in the austenite domain and further quenching by rapid cooling. The steel composition is not especially limited, however the invention is advantageously implemented with steel compositions that make it possible to obtain a yield stress higher than 1000 MPa after press hardening.
With this regard, the steel composition may contain the following elements, expressed in weight %:
These compositions make it possible to achieve different levels of yield and tensile stress after press hardening.
The precoating can be aluminum, or aluminum-based alloy (i.e. aluminum is the main element in weight percentage of the precoating) or aluminum alloy (i.e. aluminum is higher than 50% in weight in the precoating)
The steel sheet can be obtained by hot-dipping in a bath at a temperature of about 670-680° C., the exact temperature depending on the composition of the aluminium based alloy or the aluminium alloy. A preferred precoating is Al—Si which is obtained by hot-dipping the sheet in a bath comprising, by weight, from 5% to 11% of Si, from 2% to 4% of Fe, optionally from 0.0015 to 0.0030% of Ca, the remainder being Al and impurities resulting from the smelting. The features of this precoating are specifically adapted to the thermal cycles of the invention.
The precoating results directly from the hot-dip process, which means that, at this stage, no additional heat treatment is performed on the product directly obtained by hot-dip aluminizing, before the heating steps which will be detailed below.
The precoating thickness on each side of the steel coil, sheet, or blank is comprised between 10 and 35 μm. For a precoating thickness less than 10 μm, the corrosion resistance after press hardening is decreased.
If the precoating thickness is more than 35 μm, alloying with iron from the steel substrate is more difficult in the external portion of the precoating, which increases the risk of the presence of a liquid phase in the heating step immediately preceding press hardening, hence the risk of pollution of rollers in the furnaces.
After providing the non-stamped precoated steel coil, sheet or blank, it is heated in a furnace up to a temperature θ1. The furnace can be a single zone or a multizone furnace, i.e. having different zones which have their own heating means and settings. Heating can be performed by means such as radiant tubes, radiant electric resistances or by induction. The furnace atmosphere must contain at least 5% oxygen so to be able to create an alumina-containing oxide layer at the extreme surface of the steel coil, sheet or blank, as will be explained below.
It is heated up to a maximum furnace temperature θ1 comprised between 750 and 1000° C. This causes the transformation, at least partially, of the initial steel microstructure, into austenite. Below 750° C., the prealloying between the precoating and the steel substrate would be very long and not cost-efficient. Above 1000° C., the cooling following immediately θ1 could generate microstructures in the substrate with high hardness, which would make difficult some further steps, such as cutting, piercing, trimming or uncoiling. Furthermore, above 1000° C., the holding duration at this temperature must be limited in order to avoid grain coarsening and toughness decrease. If the production line stops for an unexpected reason, the blanks situated in the furnace would be held for a too long time and would be discarded, which is not cost-efficient.
The non-stamped steel coil, sheet or blank is thus maintained at temperature θ1 for a duration ti in the furnace. An interdiffusion layer, located at the interface between the pre-coating and the steel substrate is thus obtained at the end of t1. It has been experienced that the thickness of this interdiffusion layer does not significantly change during the further heating and maintain at θ2. This interdiffusion layer has a ferritic structure (α-Fe), is enriched with aluminium in solid solution, it may also include silicon in solid solution. For example, this ductile layer can contain less than 10% Al in weight and less than 4% Si in weight, the remainder being mainly Fe.
The total duration time in the furnace ti must be comprised in a range (t1min−t1max) defined as follows:
wherein θ1 is expressed in ° C. and t1min and t1max are expressed in seconds.
If the coil, sheet or blank is heated in a furnace with a unique heating zone, θ1 designates the furnace temperature. Alternatively, the coil, sheet or blank can be heated in a furnace comprising different heating zones, each zone (i) having its own temperature θ1(i). Thus, a maximum temperature θ1(max) and a minimum temperature θ1(min) are defined inside the furnace. In this case, the expression [1] is calculated by using θ1(min) and the expression [2] is calculated by using θ1(max)
When the duration t1 is less than t1min, the amount of diffusion between the steel substrate and the precoating is insufficient. Thus, there is a risk that the further heating at temperature θ3 causes the formation of liquid phase on the surface of the coating and pollution of the rollers in the furnace.
Furthermore, when heating duration is less than t1min, the thickness of the alumina-containing oxide layer which is present on the non-stamped prealloyed coil, sheet or blank, is insufficient, i.e. less is than 0.10 μm. Referring to the variation of oxygen content from the surface, this value corresponds to the full width at half maximum, as defined in “Glow Discharge Optical Emission Spectroscopy: A Practical Guide”, by T. Nellis and R. Payling, Royal Society of Chemistry, Cambridge, 2003.
Without being bound by a theory, it is believed that the formation of this superficial alumina-containing oxide layer occurs by a reaction between the adsorbed oxygen and the aluminum at the precoating surface, in the high temperature range of the whole manufacturing process of the prealloyed coil, sheet or blank. The amount of oxygen necessary for this reaction is partially generated by the decomposition of water present in the furnace atmosphere. As the decomposition of adsorbed water at the precoating surface causes the generation of adsorbed hydrogen, the hydrogen content in the steel substrate increases after the heating and holding at θ1. However, as will be explained, in a second step performed in the process, the hydrogen content will be lowered and the alumina-containing layer which has been created will make it possible that no more significant hydrogen intake will occur in a third heating step.
This alumina-containing layer can be a complex layer, i.e. for example a layer of alumina (Al2O3) topped by oxi-hydroxide alumina (AlOOH).
When t1 is outside of the range (t1min−t1max), the interdiffusion layer thickness can be outside of the 2-16 μm range. This, in turn, causes a risk that the coating structure of the final press hardened part is not well adapted to resistance spot welding, i.e. that the welding intensity range is below 1 kA.
Furthermore, when t1max is exceeded, the corrosion resistance of the final press hardened coated part tends to decrease.
After holding at θ1, the non-stamped steel coil, sheet or blank is cooled down at an intermediate temperature θi.
As the steel microstructure has been transformed, at least partially, into austenite, it is preferred that the cooling rate Vr1 is selected so to not generate hard transformation constituents such as martensite or bainite, during this cooling step. In particular, the cooling rate is selected so that the sum of the area fractions of bainite and martensite is less than 30% in the steel microstructure. To this end, Vr1 is preferably not higher than 10° C./s.
It is further even preferred that the cooling is selected so as to obtain a ferrite-pearlite microstructure which makes it possible to perform eventual operations such as cutting, trimming, piercing or uncoiling. The selection of this cooling rate can be performed for example through the implementation of a limited number of tests on a dilatometer, determining the proper critical cooling rates that make it possible to obtain such microstructural features. To this end, Vr1 is preferably not higher than 5° C./s, and more preferably not higher than 3° C./s.
Furthermore, if cooling is performed at slow rate, the growth of the alumina-containing oxide layer can continue to take place in the high temperature range.
The intermediate temperature Oi can be either room temperature, or can be higher than room temperature.
In the first case, the non-stamped steel coil, sheet or blank is thereafter heated from room temperature up to a temperature θ2 comprised between 100 and 500° C.
In the second case, the non-stamped steel coil, sheet or blank heated at θ1 is directly transferred in a furnace heated at temperature θ2 comprised between 100 and 500° C., i.e. θi=θ2. In this furnace, the atmosphere contains at least 5% oxygen.
Whatever the first or second embodiment, after maintaining at the temperature θ2 for a duration t2 comprised between 3 and 45 minutes, a non-stamped prealloyed steel coil, sheet or blank, is obtained.
The maintaining step at θ2 is also an important step in the manufacturing process: after the heating and maintaining at θ1, hydrogen is present in the steel substrate due to the adsorption at the precoating surface of the water vapor from the furnace. At this stage, the amount of diffusible hydrogen in the steel depends mainly on the dew point of the furnace atmosphere when heating at θ1, on the temperature θ1, itself and on the duration t1. The amount of diffusible hydrogen can be high due to the increased hydrogen solubility at high temperature. Values of diffusible hydrogen in the range of 0.35-0.50 ppm can be measured for example at this stage.
When the coil, sheet or blank is cooled from θ1, the hydrogen solubility decreases and hydrogen tends to desorb. However, when the temperature is less than 100° C., it has been experienced that the prealloyed coating acts as a barrier for hydrogen, thus that hydrogen desorption is very limited.
The inventors have found that maintaining the non-stamped coil, sheet or blank, in a range between 100 and 500°° C., for a duration comprised between 3 and 45 minutes, makes it possible to obtain an efficient desorption rate.
As a first preferred embodiment, the inventors have found that maintaining at a temperature θ2 higher than 400° C. and lower than 500° C., is advantageous since it makes it possible to achieve an average diffusible hydrogen content on the final press hardened coated part, less than 0.25 ppm.
As a second preferred embodiment, the inventors have found that maintaining at θ2 at a temperature higher than 100° C. and lower than 300° C. is also advantageous since it makes it possible to achieve an average diffusible hydrogen content on the final press hardened coated part, less than 0.28 ppm.
As a third preferred embodiment, the inventors have found that maintaining at θ2 at a temperature comprised between 300 and 400° C. is very advantageous, since this range makes it possible to obtain low average diffusible hydrogen with short duration time t2.
Whatever the preferred temperature range for θ2, a duration t2 comprised between 4 and 15 minutes makes it possible to obtain an average diffusible hydrogen on the final press hardened coated part, less than 0.25 ppm with a short duration, i.e. in conditions advantageous for cost production.
After maintaining at θ2, as a first alternative, the coil, sheet or blank can be cooled down to room temperature so to obtain a non-stamped prealloyed steel coil, sheet or blank. Thus, it can be stored at this temperature until further heating at temperature θ3 in the manufacturing of a press hardened part. At this stage, the prealloyed coil or sheet is cut so to obtain a non-stamped prealloyed blank, the shape contour of which is related to the geometry of the final press hardened part.
As a second alternative, the product maintained at θ2 is under the form of a prealloyed blank which can be thereafter directly heated at θ3 without cooling at room temperature.
At this stage, the prealloyed steel product is covered by a precoating wherein no free aluminum is present, i.e. aluminum is bound to other elements. The average diffusible content of this product is less than 0.35 ppm, and can be less than 0.25 ppm.
Furthermore, as will be shown below, the alumina-containing oxide layer created in the high temperature range during the previous steps makes it possible that further heating for press hardening does not cause a significant hydrogen intake.
Whatever the first or second alternative above, the non-stamped prealloyed steel blank is thereafter heated to a temperature θ3 for a total duration t3, so to obtain partial or total austenitic structure in the steel substrate. Preferably, θ3 is comprised between 850 and 1000° C.
Fast heating is performed at this step in order to limit austenite grain growth and to implement a process in very productive conditions. In this heating step, the heating duration ΔT20-700° which designates the time elapsed between 20 and 700° C., expressed in s, is less than ((26.22×th)−0.5) In this expression, th designates the thickness of the prealloyed blank, expressed in millimeters. If the blank has a variable thickness between thmin and thmax, th designates thmax.
Thanks to the prior prealloying treatment, the heating step at θ3 does not cause the formation of liquid phase in the coating. Thus, if the prealloyed blank is heated in a furnace on rollers, the pollution of the rollers by liquid, is avoided.
As no formation of liquid phase occurs, efficient heating processes can be implemented such as resistance heating, i.e. processes based on Joule effect, or induction heating. As alternative processes, heating by thermal conduction can be implemented, for example by putting in contact the prealloyed blank between two heated plates (“plate heating”) The prior prealloying suppresses the risk of molten phase presence causing sticking between the blank and the plates.
Thanks also to the prior prealloying treatment, the heating step at θ3 can be performed at a high heating rate.
Thanks also to the prior prealloying treatment, the average diffusible hydrogen increase ΔHdiff during the heating and maintaining step at θ3 is reduced to less than 0.10 ppm, and the average diffusible hydrogen content of the press hardened part is less than 0.40 ppm and can be less than 0.30 ppm.
After maintaining at θ3, the heated blank is transferred rapidly into a forming press and hot formed so to obtain a part. The part is then kept within the press tooling so as to ensure a proper cooling rate and to avoid distortions due to heterogeneities in shrinkage and phase transformations. The part mainly cools by conduction through heat transfer with the tools. The tooling can include coolant circulation so as to increase the cooling rate, or can include heating cartridges so as to lower cooling rates. Thus, the cooling rates can be adjusted precisely by taking into account the hardenability of the substrate composition through the implementation of such means. The cooling rate may be uniform in the part or may vary from one zone to another according to the cooling means, thus making it possible to achieve locally increased strength or increased ductility properties.
For achieving high tensile stress, the microstructure in the hot formed part comprises martensite or bainite. The cooling rate is chosen according to the steel composition, so as to be higher than the critical martensitic or bainitic cooling rate, depending on the microstructure and mechanical properties to be achieved. In particular, as a preferred embodiment, the microstructure contains more than 80% of martensite and/or bainite, so to take advantage of the structural hardening capacity of the steel.
Sheets of 22MnB5 steel, 1.5 mm thick, have been provided with the composition of table 1. Other elements are iron and impurities inherent in processing.
The sheets are obtained from coils which have been precoated with Al—Si through continuous hot-dipping, then cut into blanks. The precoating thickness is 25 μm on both sides. The precoating contains 9% Si in weight, 3% Fe in weight, the remainder being aluminum and impurities resulting from smelting.
The flat blanks have been subjected to different heat treatments according to the manufacturing conditions mentioned in table 2.
The heat treatment up to the temperature θ1 has been performed in a furnace under an atmosphere containing 21% oxygen while maintaining the blanks for different values of total dwell time t1. The values of t1min and t1max have been calculated from temperature θ1 according to the expressions [1] and [2] above, and the values of t1 have been compared to the range defined by t1min and t1max. After holding at this temperature, the blanks have been cooled down to room temperature by natural convection and radiation, so to obtain ferrite-pearlite microstructure. The blanks have been thereafter heated up to temperatures θ2 ranging up to 600° C. and have been maintained at this temperature for a duration t2 comprised between 4′ and 24 h, under an atmosphere containing 21% oxygen. Thus, non-stamped prealloyed blanks have been obtained.
As further comparison, a precoated steel blank has been press hardened without having undergone the prealloying treatment at θ2 and θ3. This test corresponds to reference R6 in table 2.
⊖3
No
No
600
24 h
700
95
Characteristic features of the non-stamped prealloyed blanks before heating at θ3 have been determined and reported in Table 3:
The prealloyed coated blanks have been heated up to temperature θ3 and the presence of an eventual liquid phase has been checked. If liquid phase has been present during heating, the coating surface appearance, as observed by Scanning Electron Microscope, is very smooth due to surface tension of the liquid.
At θ3=900° C., the structure of the steel is fully austenitic. The blanks have been transferred within 10 s in a press, hot formed and press hardened. Cooling in the press is performed so to ensure that the steel microstructure of the press hardened coated parts, is fully martensitic.
After press hardening, the coated steel parts are cut, polished, etched with Nital reagent and observed by optical microscope at a magnification of 500×. The coating structure is observed to determine if it displays a distinct four-layer structure adapted for resistance welding, such as described in WO2008053273, i.e. ranging from the steel substrate to the coating surface:
The press hardened coated parts have a yield stress higher than 1000 MPa.
The characteristic features of the press hardened parts are also reported in Table 3.
No
1
No
0.17
No
No
1
No
0.24
No
0.38
0.37
0.40
0.36
0.41
No
No
0.01
No
0.40
0.35
In tests I1 and I2, non-stamped prealloyed blanks have been fabricated according to the conditions of the invention, and further press hardened according to the conditions of the invention. No free aluminum is present on the prealloyed blanks. No liquid phase has been experienced during the heating at θ3 in spite of the short heating duration.
The average hydrogen intake due to the heating at θ3 is very low (0.01 ppm), as well as the average hydrogen itself (0.21 ppm). Thus, the risk of delayed fracture is much decreased due to the low hydrogen content. Furthermore, it is demonstrated that even if the blanks are left for a longer duration in the furnace (from 1′40″ to 2′30″ in trials I1 and I2), no supplementary hydrogen intake ΔHdiff occurs. Thus, even if the prealloyed blanks have to stay for a longer duration in furnace due to an unexpected event in production line, this has no detrimental consequence.
The coating structure after press hardening is similar to the one described in than WO2008053273, making it possible to achieve a wide intensity range in resistance spot welding.
In tests I3-I4, the non-stamped prealloyed blanks have been fabricated with higher θ2 temperature and shorter t2 duration than in tests I1 and I2. This makes it possible to obtain prealloyed blanks which have an average diffusible content the same or smaller (0.15-0.21 ppm) than the one in tests I1 and I2.
In tests I5-I6, according to the conditions for (θ1, t1, θ2,t 2), an alumina-containing oxide layer, 0.17 μm thick together with an average diffusible hydrogen content of 0.14 ppm, has been created. As illustrated by
These properties are obtained with high productivity conditions, i.e. with a fast heating rate Δt20-700° (s) of 35 s. The coating structure after press hardening is similar to the one described in than WO2008053273. It is also mentioned that the heat treatment step (θ3, t3) does not modify significantly the alumina-containing layer: before heating at (θ3=900° C., t3=1′40″), the alumina-containing layer has a thickness of 0.17 μm, after heating at (θ3, t3) and press hardening, the alumina-containing layer has a thickness of 0.18 μm, with similar microstructural features.
For all the tests I1-I6, the ferrite-pearlite microstructure of the prealloyed blanks makes it possible to perform piercing and cutting easily.
In the tests R1-R2, the holding time t1 is not sufficient to create an interdiffusion layer of at least 2 μm. Thus, free aluminum is present in the prealloyed blank and melting occurs on the precoating when heating at θ3. Furthermore, the alumina containing layer is insufficient to prevent significant hydrogen intake ΔHdiff during press hardening. This intake is especially high when the holding duration t3 is longer.
In the test R3, although (θ1, t1) have been chosen according to the invention, the temperature θ2 is too high. Without being bound by a theory, it is believed that this can be due to the hydrogen solubility which is still high at this temperature, or to water adsorption which is present at this temperature. As a consequence, the diffusible hydrogen content is too high in the prealloyed blank.
In the test R4, although (θ1, t1) have also been chosen according to the invention, the temperature θ2 is too low, thus hydrogen effusion is insufficient since the coating acts as a barrier for hydrogen desorption. As a consequence, the diffusible hydrogen content is too high in the prealloyed blank.
In the test R5, since (θ1, t1) are outside the conditions of the invention, the diffusible hydrogen on the prealloyed blank and the press hardened are too high, even though (θ2, t2), (θ3, t3) are according to the conditions of the invention.
In the test R6, no prealloying steps have been applied. Thus liquid phase is present during heating at θ3. Even though the average diffusible is low before heating at θ3, the thickness of its alumina-containing oxide on the top of the coating is insufficient (0.01 μm), thus the average diffusible hydrogen in the final part is not less than 0.40 ppm.
Thus, the press hardened coated steel parts manufactured according to the invention can be used with profit for the fabrication of structural or safety parts of vehicles.
| Number | Date | Country | Kind |
|---|---|---|---|
| PCT/IB2018/051546 | Mar 2018 | WO | international |
This is a Divisional of U.S. patent application Ser. No. 16/968,880 filed on Aug. 11, 2020, now published as U.S. 2020/0399734 A1, which is a National Stage Application of PCT/IB2019/051764 filed on Mar. 5, 2019 which claims priority to PCT/IB2018/051546 filed on Mar. 9, 2018, all of which are hereby included by reference herein. The invention relates to pre-alloyed steel parts, and a process for manufacturing parts, made out of aluminized precoated steel sheets which are heated, press formed and cooled so as to obtain so-called press hardened or hot press formed parts. These parts with high yield and tensile strength ensure anti-intrusion or energy-absorption functions in cars or trucks vehicles.
| Number | Date | Country | |
|---|---|---|---|
| Parent | 16968880 | Aug 2020 | US |
| Child | 18882017 | US |
