U.S. patent application number 16/485606 was filed with the patent office on 2020-05-28 for method for producing a hot-formed coated steel product.
This patent application is currently assigned to TATA STEEL IJMUIDEN B.V.. The applicant listed for this patent is TATA STEEL IJMUIDEN B.V.. Invention is credited to Petrus Cornelis Jozef BEENTJES, Hugo VAN SCHOONEVELT.
Application Number | 20200165712 16/485606 |
Document ID | / |
Family ID | 61837719 |
Filed Date | 2020-05-28 |
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United States Patent
Application |
20200165712 |
Kind Code |
A1 |
BEENTJES; Petrus Cornelis Jozef ;
et al. |
May 28, 2020 |
METHOD FOR PRODUCING A HOT-FORMED COATED STEEL PRODUCT
Abstract
An Al--Si-alloy coated steel strip for hot press forming and to
a method for producing the Al--Si-alloy coated steel strip in a
continuous coating process.
Inventors: |
BEENTJES; Petrus Cornelis
Jozef; (Castricum, NL) ; VAN SCHOONEVELT; Hugo;
(IJmuiden, NL) |
|
Applicant: |
Name |
City |
State |
Country |
Type |
TATA STEEL IJMUIDEN B.V. |
Velsen-Noord |
|
NL |
|
|
Assignee: |
TATA STEEL IJMUIDEN B.V.
Velsen-Noord
NL
|
Family ID: |
61837719 |
Appl. No.: |
16/485606 |
Filed: |
February 23, 2018 |
PCT Filed: |
February 23, 2018 |
PCT NO: |
PCT/EP2018/054600 |
371 Date: |
August 13, 2019 |
Current U.S.
Class: |
1/1 |
Current CPC
Class: |
C22C 38/14 20130101;
C23C 2/40 20130101; C22C 38/32 20130101; C23C 2/12 20130101; C22C
38/001 20130101; C21D 1/42 20130101; C22C 38/54 20130101; C23C 2/28
20130101; C22C 38/08 20130101; C22C 38/02 20130101; C22C 38/04
20130101; C22C 38/16 20130101; C22C 38/06 20130101; C23C 10/00
20130101; C22C 38/12 20130101; C21D 1/26 20130101 |
International
Class: |
C23C 2/12 20060101
C23C002/12; C22C 38/14 20060101 C22C038/14; C22C 38/16 20060101
C22C038/16; C22C 38/00 20060101 C22C038/00; C22C 38/04 20060101
C22C038/04; C23C 2/40 20060101 C23C002/40; C22C 38/12 20060101
C22C038/12; C22C 38/32 20060101 C22C038/32; C22C 38/02 20060101
C22C038/02; C22C 38/08 20060101 C22C038/08; C22C 38/06 20060101
C22C038/06; C21D 1/42 20060101 C21D001/42 |
Foreign Application Data
Date |
Code |
Application Number |
Feb 28, 2017 |
EP |
17158418.8 |
Feb 28, 2017 |
EP |
17158419.6 |
Claims
1. A process for producing a hot-formed steel product, wherein the
hot-formed product comprises a steel substrate and an aluminium
alloy coating layer, the aluminium alloy coating layer comprising a
surface layer and a diffusion layer between the surface layer and
the steel substrate, and wherein the surface layer contains between
0 and 10 area % of .tau.-phase, and wherein the .tau.-phase, if
present, is dispersed in the surface layer, and wherein the process
at least comprises the subsequent steps of: providing a steel strip
or sheet provided with an aluminium alloy coating layer by means of
immersing the steel substrate in a molten aluminium alloy bath
comprising at least 0.4 wt. % and at most 4.0 wt. % of Si; cutting
the coated steel strip or sheet to obtain a blank; hot-forming the
blank into a product by means of a direct or indirect hot-forming
process wherein the hot-forming process involves heating the blank,
or the hot-formed steel product in case of the indirect hot-forming
process, to a temperature above the Ac1-temperature, preferably
above the Ac3-temperature of the steel; cooling the product to form
the desired final microstructure to obtain the hot-formed steel
product.
2. The process according to claim 1, wherein the surface layer is
free from .tau.-phase.
3. The process according to claim 1, wherein the outermost surface
layer is free from .tau.-phase.
4. The process according to claim 1, wherein the molten aluminium
alloy bath comprises 0.6 to 4.0 wt. % of silicon.
5. The process according to claim 1, wherein the molten aluminium
alloy bath comprises 0.6 to 1.4 wt. % of silicon.
6. The process according to claim 1, wherein the molten aluminium
alloy bath comprises at least 1.6 wt. % to 4.0 wt. % of
silicon.
7. The process according to claim 1, wherein the coated steel strip
or sheet with the aluminium alloy coating layer is subjected to a
pre-diffusion annealing step before the hot-forming step.
8. The process according to claim 1, wherein the coated strip or
sheet with the aluminium alloy coating layer is subjected to a
pre-diffusion annealing step: as a strip in a hot-dip coating line
immediately following the hot-dip coating, as a strip, sheet or
blank in an induction furnace optionally in combination with a
radiation and/or convection heating oven.
9. The process according to claim 1, wherein the alloy layer on the
coated steel strip or sheet prior to heating and hot-forming, and
prior to the optional pre-diffusion annealing step, comprises at
least three distinct layers, from the steel strip surface outwards:
intermetallic layer 1, consisting of Fe.sub.2Al.sub.5 with silicon
in solid solution intermetallic layer 2, consisting of FeAl.sub.3
with silicon in solid solution outer layer having the composition
of the melt.
10. The process according to claim 1, wherein the thickness of the
aluminium alloy coating layer prior to heating and hot-forming, and
prior to the optional pre-diffusion annealing, is between 10 and 40
.mu.m.
11. The process according to claim 1, wherein the composition of
the steel strip comprises (in weight. %): TABLE-US-00008 C:
0.01-0.5 P: .ltoreq.0.1 Nb: .ltoreq.0.3 Mn: 0.4-4.0 S: .ltoreq.0.05
V: .ltoreq.0.5 N: 0.001-0.030 B: .ltoreq.0.08 Ca: .ltoreq.0.05 Si:
.ltoreq.3.0 O: .ltoreq.0.008 Ni .ltoreq.2.0 Cr: .ltoreq.4.0 Ti:
.ltoreq.0.3 Cu .ltoreq.2.0 Al: .ltoreq.3.0 Mo: .ltoreq.1.0 W
.ltoreq.0.5
the remainder being iron and unavoidable impurities.
12. A hot-formed steel product, said hot-formed product comprising
a steel substrate and an aluminium alloy coating layer comprising
at least 0.4 wt. % of Si and at most 4.0 wt. %, the aluminium alloy
coating layer comprising a surface layer and a diffusion layer
between the surface layer and substrate, and wherein the surface
layer contains between 0 and 10 area % of .tau.-phase, and wherein
the .tau.-phase is dispersed in the surface layer.
13. The hot formed product according to claim 12 having at least
one feature selected from the group consisting of: wherein the
aluminium alloy coating layer comprises 0.6 to 4.0 wt. % of
silicon, wherein the surface layer is free from .tau.-phase,
wherein the outermost surface layer is free from .tau.-phase, and
wherein the contiguity of the .tau.-phase C.sub..tau. is
.ltoreq.0.4.
14. The hot formed product according to claim 12, wherein the
composition of the steel substrate comprises (in weight. %):
TABLE-US-00009 C: 0.01-0.5 P: .ltoreq.0.1 Nb: .ltoreq.0.3 Mn:
0.4-4.0 S: .ltoreq.0.05 V: .ltoreq.0.5 N: 0.001-0.030 B:
.ltoreq.0.08 Ca: .ltoreq.0.05 Si: .ltoreq.3.0 O: .ltoreq.0.008 Ni
.ltoreq.2.0 Cr: .ltoreq.4.0 Ti: .ltoreq.0.3 Cu .ltoreq.2.0 Al:
.ltoreq.3.0 Mo: .ltoreq.1.0 W .ltoreq.0.5
the remainder being iron and unavoidable impurities.
15. A vehicle part made from the hot-formed product obtainable by
the method of claim 1.
16. The process according to claim 1, wherein the molten aluminium
alloy bath comprises at least 1.8 wt. % to 4.0 wt. % of
silicon.
17. The hot formed product according to claim 12, wherein the
composition of the steel substrate comprises (in wt. %) C:
0.10-0.25 Mn: 1.0-2.4 N: .ltoreq.0.03 Si: .ltoreq.0.4 Cr:
.ltoreq.1.0 Al: .ltoreq.1.5 P: .ltoreq.0.02 S: .ltoreq.0.005 B:
.ltoreq.0.005 O: .ltoreq.0.008 Ti: .ltoreq.0.3 Mo: .ltoreq.0.5 Nb:
.ltoreq.0.3 V: .ltoreq.0.5 Ca: .ltoreq.0.05 Ni.ltoreq.0.05
Cu.ltoreq.0.05 W.ltoreq.0.02 the remainder being iron and
unavoidable impurities.
18. The hot-formed product according to claim 13 as a part in a
vehicle, e.g. as a body part.
19. The hot formed product according to claim 12: wherein the
aluminium alloy coating layer comprises 0.6 to 4.0 wt. % of
silicon, wherein the surface layer is free from .tau.-phase,
wherein the outermost surface layer is free from .tau.-phase, and
wherein the contiguity of the .tau.-phase C.sub..tau. is
.ltoreq.0.4.
20. The vehicle part of claim 15, wherein the vehicle part is a
vehicle body part.
21. A vehicle part made from the hot-formed product made according
to claim 12.
22. The vehicle part of claim 21, wherein the vehicle part is a
vehicle body part.
Description
[0001] The invention relates to an Al--Si-alloy coated steel strip
for hot press forming and to a method for producing the
Al--Si-alloy coated steel strip in a continuous coating
process.
[0002] From EP0971044 it is known to use aluminium-silicon coated
steel strip in producing hot-press-formed (hot forming) or
press-hardened articles. In this process a blank, cut from the
steel strip, is heated to a temperature at which the steel has
transformed to austenite (i.e. above the Ac1-temperature), and is
easy to form into the desired shape. After pressing the austenitic
strip into the desired shape it is cooled at a cooling rate that
allows the austenite to transform to martensite or other hardening
structures, resulting in a formed article with high strength.
EP2377965 discloses that strengths equal to or more than 1000 MPa
can be achieved in a steel sheet, such as a sheet or 22MnB5. The
aluminium-silicon coating intends to protect the strip against
oxidation and decarburization during its stay at high temperature
and the subsequent cooling. The finished hot-press formed part does
not require removal of surface oxide, and the part can be processed
further. The aluminium-silicon coating currently used in practice
contains about 10% silicon.
[0003] A disadvantage of the aluminium-silicon coating with 10%
silicon is that the paint adhesion on the final part after hot
forming and cooling is inadequate. Significant flaking off of the
paint is frequently observed.
[0004] It is a further object of the invention to provide an
aluminium-silicon coated steel strip with an improved paint
adherence after hot forming.
[0005] It is a further object of the invention to provide a method
for producing said aluminium-silicon coated steel strip.
[0006] It is moreover an object of the invention to provide the use
of the above mentioned steel strip to the advantage of the
hot-forming process.
[0007] It is furthermore an object of the invention to provide the
product resulting from the use of the steel strip according to the
invention.
[0008] According to a first aspect of the invention a process is
provided for producing a hot-formed steel product, wherein the
hot-formed product comprises a steel substrate and an aluminium
alloy coating layer, the aluminium alloy coating layer comprising a
surface layer and a diffusion layer between the surface layer and
the steel substrate, and wherein the surface layer contains between
0 and 10 area % of .tau.-phase, and wherein the .tau.-phase, if
present, is dispersed in the surface layer, and wherein the process
at least comprises the subsequent steps of: [0009] providing a
steel strip or sheet provided with an aluminium alloy coating layer
by means of immersing the steel substrate in a molten aluminium
alloy bath comprising at least 0.4 wt. % of Si and at most 4.0 wt.
% of Si; [0010] cutting the coated steel strip or sheet to obtain a
blank; [0011] hot-forming the blank into a product by means of the
direct hot-forming process or indirect hot-forming process wherein
the hot-forming process involves heating the blank, or the
hot-formed steel product in case of the indirect hot-forming
process, to a temperature above the Ac1-temperature, preferably
above the Ac3-temperature of the steel; [0012] cooling the product
to form the desired final microstructure to obtain the hot-formed
steel product.
[0013] The coated steel strip according to the invention provides
good protection against oxidation during the hot forming on the one
hand, and provides excellent paint adhesion of the finished part on
the other. It is important that if there is .tau.-phase present in
the surface layer that it is present in the form of embedded
islands, i.e. a dispersion, and not as a continuous layer. A
dispersion is defined as a material comprising more than one phase
where at least one of the phases (the dispersed phase) consists of
finely divided phase domains embedded in the matrix phase.
[0014] The improvement of the paint adherence is the result of the
absence or the limited presence of .tau.-phase which the inventors
found to be responsible for the bad adhesion of the known coatings.
Within the context of this invention, a phase is considered to be a
.tau.-phase if the composition is in the following range
Fe.sub.xSi.sub.yAl.sub.z phase with a composition range of 50-70
wt. % Fe, 5-15 wt. % Si and 20-35 wt. % Al. .tau.-phase form when
the solubility of silicon is exceeded as a result of the diffusion
of iron into the aluminium layer. As a result of the enrichment
with iron, the solubility of silicon is exceeded and .tau.-phase,
such as Fe.sub.2SiAl.sub.2, form. This occurrence imposes
restrictions to the duration of the annealing and the height of the
annealing temperature during the hot-forming process. So the
formation of .tau.-phase can be easily avoided or restricted
primarily by controlling the silicon content in the aluminium alloy
layer on the steel strip or sheet and secondarily by the annealing
temperature and time. The added advantage of this is that the
duration of the blanks in the furnace can be reduced as well, which
may allow shorter furnaces, which is an economical advantage. The
combination of annealing temperature and time for a given coating
layer is easily determined by simple experimentation followed by
routine microstructural observation (see below in the examples). It
should be noted that the percentage of .tau.-phase is expressed in
area %, because the fraction is measured on a cross section of the
coating layer.
[0015] There are two variants of hot forming: direct and indirect
hot stamping. The direct process starts with a coated blank that is
heated and formed, while the indirect process uses a preformed
component from a coated blank that is subsequently heated and
cooled to obtain the desired properties and microstructure after
cooling. From a productivity perspective the direct process is
preferable. Within the context of this invention both direct and
indirect hot stamping are deemed to be part of the invention
wherein the feature `hot-forming the blank into a product` can be
direct or indirect hot forming. In the indirect hot forming process
the order is forming the blank into the formed product--heating the
formed product in a furnace to a temperature sufficiently high for
the steel to transform into austenite--cooling the formed product
to obtain the desired final microstructure of the product, whereas
in the direct hot forming process the order is heating the blank in
a furnace to a temperature sufficiently high for the steel to
transform into austenite heating--hot-forming the blank in a die to
obtain a hot-formed product--cooling the hot-formed product to
obtain the desired final microstructure of the product.
[0016] In an embodiment of the invention the surface layer is free
from .tau.-phase. Because of the influence of the presence of
.tau.-phase on paint adhesion, it is preferable that there is no
.tau.-phase in the surface layer, or at least no .tau.-phase in the
outermost surface layer. Although the meaning of outermost surface
layer should be perfectly clear, superfluously it is explained in
FIG. 1B.
[0017] The inventors found that this can be obtained by providing
an aluminium alloy coating layer on a steel substrate which
comprises at least 0.4 wt. % of silicon. Preferably the aluminium
alloy coating layer comprises at least 0.6 and/or at most 4.0 wt. %
of silicon.
[0018] It was found that the contiguity of the .tau.-phase after
hot forming in the aluminium alloy coating layer according to the
invention is preferably at most 0.4. This means that the
.tau.-phase, if present, is not a closed layer, but a dispersion.
As the amount of .tau.-phase is at most 10%, the combination of
continguity and amount reveals a dispersed presence of .tau.-phase
if t-phase is present. It is noted that it is preferable that no
.tau.-phase is present, and this appears to be the case for hot
formed aluminium alloy coated steel strips with a silicon content
in the aluminium alloy of less than 2.5%.
[0019] Contiguity (C) is a property used to characterize
microstructure of materials. It quantifies the connected nature of
the phases in a composite and can be defined as the fraction of the
internal surface of an .alpha. phase shared with other .alpha.
phase particles in an .alpha.-.beta. two-phase structure. The
contiguity of a phase varies between 0 and 1 as the distribution of
one phase in the other changes from completely dispersed structure
(no .alpha.-.alpha. contacts) to a fully agglomerated structure
(only .alpha.-.alpha. contacts). The interfacial areas can be
obtained using a simple method of counting intercepts with phase
boundaries on a polished plane of the microstructure and the
contiguity can be given by the following equations: where C.alpha.
and C.beta. are the contiguity of the .alpha. and .beta. phases,
N.sub.L.sup..alpha..alpha. and N.sub.L.sup..beta..beta. are the
number of intercepts of .alpha./.alpha. and .beta./.beta.
interfaces, respectively, with random line of unit length, and
N.sub.L.sup..alpha..beta. is the number of .alpha./.beta.
C .alpha. = 2 N L .alpha..alpha. 2 N L .alpha..alpha. + N L
.alpha..beta. ##EQU00001## C .beta. = 2 N L .beta..beta. 2 N L
.beta..beta. + N L .alpha..beta. ##EQU00001.2##
interfaces with a random line of unit length. With a contiguity
C.sub..alpha. of 0, there are no .alpha.-grains touching other
.alpha.-grains. With a contiguity C.sub..alpha. of 1, all
.alpha.-grains touch other .alpha.-grains, meaning that there is
just one big lump of .alpha.-grains embedded the .beta.-phase.
[0020] Preferably the contiguity of the .tau.-phase in the surface
layer, if present, is less than C.sub..tau. is .ltoreq.0.4.
[0021] The aluminium alloy layer provided on the steel strip or
sheet comprises of aluminium, silicon and iron alloys and
intermetallics thereof, which means that the alloy layer consists
substantially of aluminium, silicon and iron alloys and
intermetallics thereof, but that there may be other intended
constituents like iron and unintended constituents like inevitable
impurities present in the alloy layer. These unintended
constituents are insignificant amounts of inevitable impurities,
but also elements like manganese and chromium which are the result
of dissolution of these elements from the steel strip or sheet
passing through the melt in the hot dip coating installation. This
dissolution process is unavoidable and the presence of these
dissolved elements is inevitable. It will be clear that these
elements also end up in the aluminium alloy coating layer deposited
on top of the steel strip or sheet.
[0022] It is noted that some elements are known to be added to the
melt for specific reasons: Ti, B, Sr, Ce, La, and Ca are elements
used to control grain size or modify the aluminium-silicon
eutectic. Mg and Zn can be added to the bath to improve corrosion
resistance of the final hot-formed product. As a result, these
elements may also end up in the aluminium alloy coating layer.
Preferably the Zn content and/or the Mg content in the molten
aluminium alloy bath is below 1.0 wt % to prevent top dross.
Elements like Mn, Cr, Ni and Fe will also likely be present in the
molten aluminium alloy bath as a result of dissolution of these
elements from the steel strip passing through the bath, and thus
may end up in the aluminium alloy coating layer. A saturation level
of iron in the molten aluminium alloy bath is typically between 2
and 3 wt. %. So in the method according to the invention the
aluminium alloy coating layer typically contains dissolved elements
from the steel substrate such as manganese, chromium and iron up to
the saturation level of these elements in the molten aluminium
alloy bath.
[0023] It is noted that the steel strip or sheet may be a
hot-rolled steel strip or sheet of suitable thickness and
composition for hot forming or a cold-rolled steel strip or sheet
of suitable thickness and composition for hot forming. The
cold-rolled steel strip or sheet may have a full-hard
microstructure, a recovered microstructure or a recrystallised
microstructure prior to hot-dip coating.
[0024] The inventors found that this hot forming method can be used
with any steel grade that results in improved properties after the
cooling of the hot-formed product. Examples of these are steels
that result in a martensitic microstructure after cooling from the
austenitic range at a cooling rate exceeding the critical cooling
rate. However, the microstructure after cooling may also comprise
mixtures of martensite and bainite, mixtures of martensite,
retained austenite and bainite, mixtures of ferrite and martensite,
mixtures of martensite, ferrite and bainite, mixtures of
martensite, retained austenite, ferrite and bainite, or even
ferrite and very fine pearlite.
[0025] In an embodiment of the invention the steel strip has a
composition comprising (in wt. %)
TABLE-US-00001 C: 0.01-0.5 P: .ltoreq.0.1 Nb: .ltoreq.0.3 Mn:
0.4-4.0 S: .ltoreq.0.05 V: .ltoreq.0.5 N: 0.001-0.030 B:
.ltoreq.0.08 Ca: .ltoreq.0.05 Si: .ltoreq.3.0 O: .ltoreq.0.008 Ni
.ltoreq.2.0 Cr: .ltoreq.4.0 Ti: .ltoreq.0.3 Cu .ltoreq.2.0 Al:
.ltoreq.3.0 Mo: .ltoreq.1.0 W .ltoreq.0.5
the remainder being iron and unavoidable impurities. These steels
allow very good mechanical properties after a hot-forming process,
whereas during the hot forming above Ac1 or Ac3 they are very
formable. Preferably the nitrogen content is at most 0.010%. It is
noted that any one or more of the optional elements may also be
absent. i.e. either the amount of the element is 0 wt. % or the
element is present as an unavoidable impurity.
[0026] In a preferable embodiment the carbon content of the steel
strip is at least 0.10 and/or at most 0.25%. In a preferable
embodiment the manganese content is at least 1.0 and/or at most
2.4%. Preferably the silicon content is at most 0.4 wt. %.
Preferably the chromium content is at most 1.0 wt. %. Preferably
the aluminium content is at most 1.5 wt. %. Preferably the
phosphorus content is at most 0.02 wt. %. Preferably the sulphur
content is at most 0.005 wt. %. Preferably the boron content is at
most 50 ppm. Preferably the molybdenum content is at most 0.5 wt.
%. Preferably the niobium content is at most 0.3 wt. %. Preferably
the vanadium content is at most 0.5 wt. %. Preferably nickel,
copper and calcium are under 0.05 wt. % each. Preferably tungsten
is at most 0.02 wt %. These preferable ranges can be used in
combination with the steel strip composition as disclosed above
individually or in combination.
[0027] In a preferred embodiment the steel strip has a composition
comprising (in wt. %)
TABLE-US-00002 C: 0.10-0.25 P: .ltoreq.0.02 Nb: .ltoreq.0.3 Mn:
1.0-2.4 S: .ltoreq.0.005 V: .ltoreq.0.5 N: .ltoreq.0.03 B:
.ltoreq.0.005 Ca: .ltoreq.0.05 Si: .ltoreq.0.4 O: .ltoreq.0.008 Ni
.ltoreq.0.05 Cr: .ltoreq.1.0 Ti: .ltoreq.0.3 Cu .ltoreq.0.05 Al:
.ltoreq.1.5 Mo: .ltoreq.0.5 W .ltoreq.0.02
the remainder being iron and unavoidable impurities. Preferably the
nitrogen content is at most 0.010%. Typical steel grades suitable
for hot forming are given in table A.
TABLE-US-00003 TABLE A Typical steel grades suitable for hot
forming Steel C Si Mn Cr Ni Al Ti B N C.sub.eq B-A 0.07 0.21 0.75
0.37 0.01 0.05 0.048 0.002 0.006 0.148 B-B 0.16 0.40 1.05 0.23 0.01
0.04 0.034 0.001 -- 0.246 B-C 0.23 0.22 1.18 0.16 0.12 0.03 0.04
0.002 0.005 0.320 B-D 0.25 0.21 1.24 0.34 0.01 0.03 0.042 0.002
0.004 0.350 B-E 0.33 0.31 0.81 0.19 0.02 0.03 0.046 0.001 0.006
0.400 N-A 0.15 0.57 1.45 0.01 0.03 0.04 0.003 -- 0.003 0.243 N-B
0.14 0.12 1.71 0.55 0.06 0.02 0.002 -- -- 0.258 N-C 0.19 0.55 1.61
0.02 0.05 0.04 0.003 -- 0.006 0.291 N-D 0.20 1.81 1.48 0.04 0.03
0.04 0.006 -- -- 0.337
[0028] In an embodiment of the invention the surface layer is free
from .tau.-phase. The inventors found that when the surface layer
is free from .tau.-phase that the paint adhesion to the product is
better than the known product provided with the known
aluminium-silicon coating containing about 10% silicon. It should
be noted that local variations in composition may lead to the
occasional occurrence of .tau.-phase in the surface layer, and that
this does not immediately lead to a steep decline in paint
adhesion, but it is certainly important to note that the ideal case
is that there is no .tau.-phase in the surface layer.
[0029] In an embodiment of the invention the outermost surface
layer is free from .tau.-phase. The inventors found that it is
important that the surface layer is free from .tau.-phase to obtain
a good paint adhesion to the product. It should be noted that local
variations in composition may lead to the occasional occurrence of
.tau.-phase at the outermost surface layer, and that this does not
immediately lead to a steep decline in paint adhesion, but it is
certainly important to note that the ideal case is that there is no
.tau.-phase at the surface.
[0030] In a embodiment of the invention the aluminium alloy coating
layer comprises 0.6 to 4.0 wt. % of silicon, the balance being
aluminium and inevitable elements and impurities consistent with
the hot dip coating process. By limiting the silicon content to
these values the occurrence of .tau.-phase in the surface layer
and/or at the outermost surface layer is achievable. The
combination of silicon content in the hot-dip coated aluminium
alloy coating layer, the annealing temperature and time for this
alloy layer is easily determined by simple experimentation followed
by routine microstructural observation (see below in the
examples).
[0031] In a preferred embodiment of the invention the aluminium
alloy coating layer contains 0.6 to 1.4 wt. % of silicon. No
.tau.-phase will occur after hot forming in these layers. This
embodiment is particularly suitable for thick coating layers,
typically of more than 20 .mu.m.
[0032] In a preferred embodiment of the invention the aluminium
alloy coating layer contains at least 1.6% to 4.0 wt. % of silicon,
preferably at least 1.8% wt. % Si. Preferably the aluminium alloy
coating layer contains at most about 2.9 wt. % Si, more preferably
at most 2.7, and an even more preferable maximum is 2.5%. With the
higher silicon content the risk of formation of some .tau.-phase in
the surface layer or at the outermost surface layer after hot
forming increases somewhat, but by controlling the annealing
temperature and time this can be easily prevented or mitigated.
With a silicon content in the aluminium alloy coating layer between
1.6 to 2.9 wt. % or any one of the preferable ranges cited
hereinabove a robust processing window is obtained. This embodiment
is particularly suitable for thinner coating layers, typically of
20 .mu.m or thinner.
[0033] In an embodiment of the invention the hot-dip coated steel
strip or sheet is subjected after coating to a pre-diffusion
treatment, i.e. a pre-diffusion annealing step. This shortens the
hot-forming step in the sense that the diffusion of iron into the
aluminium alloy coating layer has already happened and that the
aluminium alloy coating layer has been converted into a
fully-alloyed Al--Fe--Si coating layer consisting essentially of
iron-aluminides with silicon in solid solution together with an
upper layer of iron-aluminium intermetallics. It may also improve
consistency of the product because the pre-diffusion treatment may
be performed in a more controlled environment, e.g. in a separate
continuous annealing line, or in-line in an annealing section
immediately following the hot dip coating step, or in a separate
heating step connected to the heating furnace prior to the hot
stamping process. This allows the use of an induction furnace
rather than a radiation furnace for annealing the blanks prior to
hot-forming because diffusion annealing of the coating according to
the invention is very fast. If the coating is not pre-diffused,
then the outer layer of the coating still has the composition of
the molten aluminium bath, and using induction heating could cause
the outer layer to melt and interact with the diffusion field
potentially resulting in a coating shift or a wavy surface.
[0034] Also, the reflectivity of the pre-diffused fully-alloyed
aluminium-iron-silicon coated steel strip is much lower which is
the reason for the faster heating of blanks if a radiation furnace
is used, and thus to potentially fewer or smaller reheating
furnaces, and less damage of the product and pollution of the
equipment due to roll build-up. The Fe.sub.2Al.sub.5 phase on the
surface is darker in colour, and this causes the lower reflectivity
and the higher absorption of heat in a radiation furnace.
[0035] In addition, other heating means, like induction heating and
infrared heating means can be used for very fast heating. These
heating means can be used in a stand-alone situation or as a fast
heating step prior to a short radiation furnace.
[0036] In an embodiment wherein the coated strip or sheet with the
aluminium alloy coating layer is subjected to a pre-diffusion
annealing step: [0037] as a strip in a hot-dip coating line by
continuous annealing immediately following the hot-dip coating;
[0038] as a strip in a continuous annealing line after the strip
was cooled down to ambient temperature; [0039] as a strip, sheet or
blank in an induction furnace optionally in combination with a
radiation and/or convection heating oven.
[0040] In an embodiment of the invention the aluminium alloy
coating layer on the coated steel strip or sheet after hot dipping
and cooling comprises at least three distinct layers, as seen from
the steel substrate outwards: [0041] intermetallic layer 1,
consisting of Fe.sub.2Al.sub.5 phase with Si in solid solution;
[0042] intermetallic layer 2, consisting of FeAl.sub.3 phase with
Si in solid solution; [0043] outer layer, solidified
aluminium-alloy with the composition of the molten aluminium alloy
bath, i.e. including the inevitable presence of impurities and
dissolved elements from the preceding strips. Although ideally the
intermetallic layers consist only of the mentioned compounds, it is
possible that there may be insignificant amounts of other
components present as well as inevitable impurities or intermediate
compounds. The dispersed .tau.-phase at higher silicon contents
would be one such inevitable compound. However, these insignificant
amounts have been found to have no adverse effects on the
properties of the coated steel substrate.
[0044] The preferred method to produce the coated steel strip is to
immerse a suitably prepared cold-rolled strip in a molten aluminium
alloy bath containing at least 0.4% Si, and preferably of at least
0.6 and/or at most 4.0% of silicon held at a temperature between
its melting temperature and 750.degree. C., preferably at least
660.degree. C. and/or preferably at most 700.degree. C. The
residence time of the strip in the melt is preferably at least 2
seconds and preferably at most 10 seconds. There is a direct link
between the residence time, length of the liquid trajectory and the
line speed. The length of the liquid trajectory is typically about
6 m, which corresponds to line speeds of 180-36 m/min for residence
times of between 2 and 10 s. The strip entry temperature in the
bath is between 550 and 750.degree. C., preferably at least
630.degree. C., and more preferably at least 660.degree. C. and/or
preferably at most 700.degree. C. Preferably the strip temperature
is about the same as that of the melt to avoid heating or cooling
of the bath.
[0045] In an embodiment of the invention the thickness of the alloy
layer prior to heating and hot-forming (i.e. the layer "as-coated")
is between 10 and 40 .mu.m. So the process results in a thickness
of the aluminium alloy coating layer prior to heating and
hot-forming, and prior to the optional pre-diffusion annealing, of
between 10 and 40 .mu.m
[0046] In an embodiment of the invention the thickness of the
aluminium alloy coating layer prior to heating and hot-forming, and
prior to the optional pre-diffusion annealing, is at least 12 .mu.m
and/or at most 30 .mu.m.
[0047] In an embodiment of the invention the thickness of the alloy
layer prior to heating and hot-forming, and prior to the optional
pre-diffusion annealing, is at least 13 .mu.m, and/or at most 25
.mu.m, preferably at most 20 .mu.m.
[0048] According to a second aspect the invention is also embodied
in a hot-formed steel product, produced according to the method
according to the invention, such as, but not limited to, a
hot-formed steel product, said hot-formed product comprising a
steel substrate and an aluminium alloy coating layer, the aluminium
alloy coating layer comprising a surface layer, and a diffusion
layer between the surface layer and substrate, and wherein the
surface layer contains between 0 and 10 area % of .tau.-phase, and
wherein the .tau.-phase is dispersed in the surface layer.
[0049] The invention is also embodied in a hot formed product as
described above wherein:
[0050] 1. the aluminium alloy coating layer comprises at least 0.4
wt. % of silicon, and/or wherein
[0051] 2. the surface layer of the aluminium alloy coating layer is
free from .tau.-phase and/or wherein
[0052] 3. the outermost surface layer of the aluminium alloy
coating layer is free from .tau.-phase.
[0053] So any one of these three conditions may be fulfilled, or
any combination of two conditions, or all of them.
[0054] Preferably, if there is .tau.-phase present in the surface
layer, the contiguity of the .tau.-phase in the surface layer,
C.sub..tau., is .ltoreq.0.4.
[0055] The inventors found that this can be obtained by providing
an aluminium alloy coating layer on a steel substrate which
comprises at least 0.4 wt. % of silicon. Preferably the aluminium
alloy coating layer comprises at least 0.6 and/or at most 4.0 wt. %
of silicon.
[0056] In a preferred embodiment of the invention the aluminium
alloy coating layer contains 0.6 to 1.4 wt. % of silicon. No
.tau.-phase will occur after hot forming in these layers. This
embodiment is particularly suitable for thick coating layers,
typically of more than 20 .mu.m.
[0057] In a preferred embodiment of the invention the aluminium
alloy coating layer contains at least 1.6% to 4.0 wt. % of silicon,
preferably at least 1.8% wt. % Si. Preferably the aluminium alloy
coating layer contains at most about 2.9 wt. % Si, more preferably
at most 2.7, and an even more preferable maximum is 2.5%. With the
higher silicon content the risk of formation of some .tau.-phase in
the surface layer or at the outermost surface layer after hot
forming increases somewhat, but by controlling the annealing
temperature and time during the hot-forming process this can be
prevented or mitigated. With a silicon content in the aluminium
alloy coating layer between 1.6 to 2.9 wt. % or any one of the
preferable ranges cited hereinabove a robust processing window is
obtained. This embodiment is particularly suitable for thinner
coating layers, typically of 20 .mu.m or thinner.
[0058] The invention will now be further described by means of the
following, non-limiting, examples.
[0059] In FIG. 1A the process according to the invention is
summarised. The steel strip is passed through an optional cleaning
section to remove the undesired remnants of previous processes such
as scale, oil residue etc. The clean strip is then led though the
optional annealing section, which in case of a hot rolled strip may
only be used for heating the strip to allow hot-dip coating
(so-called heat-to-coat cycle) or in case of a cold-rolled strip
may be used for a recovery or recrystallisation annealing. After
the annealing the strip is led to the hot-dip coating stage where
the strip is provided with the aluminium alloy coating layer
according to the invention. Thickness control means for controlling
the thickness of the aluminium alloy coating layer are shown
disposed between the hot-dip coating stage and the subsequent
optional pre-diffusion annealing stage. In the optional
pre-diffusion annealing stage the aluminium alloy coating layer is
transformed into a fully-alloyed aluminium-iron-silicon layer. If
no pre-diffusion annealing treatment is executed, then the alloying
condition of the aluminium alloy coating layer upon coiling will be
pretty much the same as the aluminium alloy coating layer
immediately after having passed the thickness controlling means.
The coated strip (whether optionally pre-diffused or not) is
post-processed (such as optional temper rolling or tension
levelling) before being coiled. The cooling of the coated strip
after the thickness controlling means usually takes place in two
steps, wherein the cooling immediately after the thickness
controlling means is intended to prevent any sticking or damage of
the aluminium alloy coating layer to turning rolls, and is usually
executed with an air or mist cooling at a cooling rate of about
between 10 and 30.degree. C./s and further on in the line the strip
with the aluminium alloy coating layer is cooled quickly, usually
by quenching in water. It is noted that the effect of the cooling
is largely thermal to prevent damage to the line and the aluminium
alloy coating layer, and that the effect of the cooling on the
properties of the steel substrate are negligible. The strip or
sheet produced in accordance with FIG. 1A (i.e. as-coated or
pre-diffused) can then be used in a hot-forming process according
to the invention.
[0060] In FIG. 1B a close-up of the layer structure after the
hot-forming process is shown with the surface layer and the
diffusion layer clearly identified. Also clearly visible is the
original interface between the steel substrate and the aluminium
alloy coating layer "as coated" (d.sub.0) and the increase of the
thickness after the annealing in the hot forming process (d.sub.a).
The diffusion layer has grown into the steel substrate and
therefore d.sub.0<d.sub.a. The layer structure of the surface
layer is not shown, because this is dependent on the annealing
temperature, annealing time and composition of the aluminium alloy
coating layer. The definition of outermost surface layer is
schematically indicated.
EXAMPLES
[0061] Hot-formed coated steel products were produced from a steel
substrate having the composition as given in Table 1.
TABLE-US-00004 TABLE 1 Composition of steel substrate, balance Fe
and inevitable impurities. 1.5 mm, cold-rolled, full-hard
condition. C Mn Cr Si P S Al B Ca wt. % wt. % wt. % wt. % wt. % wt.
% wt. % ppm ppm 0.20 2.18 0.64 0.055 0.010 0.001 0.036 0 17
[0062] Aluminium alloy coating layers were provided onto the steel
substrate by immersing the substrate in a molten aluminium alloy
bath (a.k.a. hot-dipping or hot-dip coating), and the silicon
content of the bath, and thus the aluminium alloy coating layers
was 1.1 and 9.6 wt. % respectively. The bath temperature was
700.degree. C., the immersion time was 3 seconds, and the thickness
of the aluminium alloy coating layers was 30 .mu.m.
[0063] After applying the coating, sheets of steel were heated for
6 minutes in a radiation furnace at a temperature of 925.degree. C.
At the end of heating the blanks were transferred in less than 10
seconds to a press and subsequently stamped and quenched. After hot
stamping the steels were covered with an aluminium alloy coating
layer of 40-50 .mu.m thickness. The increase of the thickness of
the aluminium alloy coating layer is caused by the diffusion and
alloying processes taking place in the surface layer and by the
formation of the diffusion layer between the surface layer and the
steel substrate. This diffusion layer is formed by diffusion of
aluminium into the steel substrate, thereby enriching the steel
substrate with aluminium to a level that the steel substrate
locally does not transform to austenite any longer, and stays
ferritic during the hot stamping and this ductile layer stops any
surface cracks from reaching the steel substrate. The coating of
the steel coated with a 1.1% Si layer (Sample A) consists of three
layers while in the coating of the steel coated with the 9.6% Si
(Sample B) four layers can be distinguished, as illustrated in FIG.
4. In sample B the presence of a continuous layer of .tau.-phase in
the aluminium alloy coating layer (indicated with 3 in FIG. 4) as
well as significant amounts of the same phase on the surface can be
identified.
[0064] Energy-dispersive X-ray spectroscopy (EDX or EDS), is an
analytical technique used for the elemental analysis or chemical
characterization of a sample. It relies on an interaction of some
source of X-ray excitation and a sample. Its characterization
capabilities are due in large part to the fundamental principle
that each element has a unique atomic structure allowing a unique
set of peaks on its electromagnetic emission spectrum[2] (which is
the main principle of spectroscopy). To stimulate the emission of
characteristic X-rays from a specimen or a beam of X-rays, is
focused into the sample being studied. At rest, an atom within the
sample contains ground state (or unexcited) electrons in discrete
energy levels or electron shells bound to the nucleus. The incident
beam may excite an electron in an inner shell, ejecting it from the
shell while creating an electron hole where the electron was. An
electron from an outer, higher-energy shell then fills the hole,
and the difference in energy between the higher-energy shell and
the lower energy shell may be released in the form of an X-ray. The
number and energy of the X-rays emitted from a specimen can be
measured by an energy-dispersive spectrometer. As the energies of
the X-rays are characteristic of the difference in energy between
the two shells and of the atomic structure of the emitting element,
EDS allows the elemental composition of the specimen to be measured
(https://en.wikipedia.org/wiki/Energy-dispersive_X-ray_spectroscopy).
[0065] Energy Dispersive X-ray analysis (EDX or EDS) of the sub
layers revealed the following structure for sample A: [0066] layer
1: Diffusion layer [0067] layer 2: FeAl.sub.2 (46-52 wt. % Fe,
44-50 wt. % Al and <3 wt. % Si) [0068] layer 3: Fe.sub.2Al.sub.5
(40-47 wt. % Fe, 51-58 wt. % Al and <3 wt. % Si) In the four
layered structure of sample B the identified phases were: [0069]
layer 1: Diffusion layer [0070] layer 2: Fe.sub.2Al.sub.5 [0071]
layer 3: .tau.-phase (Fe.sub.2SiAl.sub.2) [0072] layer 4:
Fe.sub.2Al.sub.5 Note that these layer structures are dependent on
the annealing time. After prolonged annealing the composition of
layer 2 of sample B will likely become FeAl.
[0073] In addition both layers contain low concentrations Cr and
Mn. EPMA line scans on cross sections of the steel coated with
Al-1.1 wt. % Si revealed Cr and Mn diffused from the substrate into
the layers. Concentrations found in the coating are about 50% of
the concentration in the substrate. An example is given in FIG. 7
for heat treatment of 6 minutes at 900.degree. C. It is noted that
intermetallic layer 1 can be very thin, even almost absent for
short and/or low annealing temperatures (see FIG. 8).
[0074] On the hot formed panels an E-coat was applied by the
following process steps:
TABLE-US-00005 Time Temperature Process step Agent [s] [.degree.
C.] Alkaline degreasing Gardoclean S5176 90 55 Spray rinsing Tap
water 60 room Activating Gardolene V6513 60 24 Phosphating
Gardobond 24 TA 180 51 Dip rinsing Deionised water 60 room
E-coating Guard 900 BASF 300 32 Dip rinsing Deionised water 60 room
Drying n.a. 30 room Curing n.a. 1380 160
[0075] E-coat adhesion of four sheets of sample A and B was tested
by immersion of the panels in deionised water of 50.degree. C.
during 10 days. After removing the panels from the warm water bath
a cross hatch pattern per sheet was made according NEN-EN-ISO 2409
(June 2007). Paint adhesion was tested on the cross-cut area by a
tape peel off test as described in aforementioned standard. Test
results were ranked according table 1 of this standard.
[0076] The four sheets of sample A exhibit excellent paint
adhesion. The edges of the cuts are completely intact and none of
the squares of the lattice is detached (FIG. 5). Therefore the
adhesion performance is rated as 0. The four sheets of sample B
show a poor paint adhesion. The rating varies between 2 and 4,
meaning cross-cut areas of 15 to 65% have flaked off.
[0077] A typical test to determine whether a coated product meets
the automotive manufacturer's requirements is the scribe undercreep
test. In this test loss of E-coat adhesion due to corrosive
creepback at a deliberately made scribe is determined. These test
results are considered to be an indicator for cosmetic corrosion in
service. E-coated sheets used for this test were produced according
the route described above. Scribes were made on the sheets through
the E-coat and metallic coating just into the substrate. Two types
of scribes per panel were made, one with a Sikkens tool and one
with a van Laar knife. Sheets were tested in a corrosion cabinet
using the VDA233-102 accelerated corrosion test. Corrosive
creepback from the scribe lines was evaluated after 10 weeks of
testing. Average creepback width was determined over a scribe
length of 70 mm. As a measurement tool rectangular transparent
templates with a length of 70 mm and a varying width in steps of
0.5 mm from 1 to 15 mm were used. The width of the template with an
area matching best with the delaminated area was taken as average
creepback width. Four sheets of sample A and of B were scribed and
tested. The results showed a significant improvement of undercreep
resistance of A compared to B. Measured undercreep on A range from
3 to 4 mm while on B values between 7 and 10.5 mm were found.
[0078] In another example aluminium coating layers were provided
onto the 1.5 mm cold-rolled full hard steel substrate by hot
dipping, and the silicon content of the coating bath was 1.9 wt. %
and 9.8 wt % respectively. The coating bath temperature was
690.degree. C., the immersion time was 5 seconds, and the resulting
layer thickness was adjusted from 15 to 25 .mu.m, as indicated in
the following table.
TABLE-US-00006 TABLE 2 Si bath concentration, layer thickness and
furnace conditions. Bath Si Layer thickness Furnace T Furnace t
Series Sheet id [wt %] [.mu.m] [.degree. C.] [minutes] 1 617024 1.9
15 925 3.5 617025 1.9 15 925 3.5 617026 1.9 15 925 3.5 2 633037 9.8
15 925 4.5 633038 9.8 15 925 4.5 633039 9.8 15 925 4.5 3 633022 9.8
25 925 6.0 633023 9.8 25 925 6.0 633025 9.8 25 925 6.0
TABLE-US-00007 TABLE 3 Paint adhesion rating Paint Bath Si Area
.tau. adhesion Series Sheet id [wt %] [%] C.tau. rating 1 617024
1.9 0 0 1 617025 1.9 0 0 1 617026 1.9 0 0 1 2 633037 9.8 >10 1 3
633038 9.8 >10 1 2-3 633039 9.8 >10 1 2 3 633022 9.8 >10 1
2 633023 9.8 >10 1 3 633025 9.8 >10 1 3
[0079] After coating application the sheets of steel were heated
for 3.5 to 6 minutes, depending on coating thickness and Si level,
in a radiation furnace at a temperature of 925.degree. C. At the
end of heating the blanks were transferred in less than 10 seconds
to a press and subsequently stamped and quenched. After hot
stamping the metallic coating layer was measured and was between
20-50 .mu.m.
[0080] After stamping the coating of the steel coated with a 1.9%
Si layer is completely free of Fe.sub.2SiAl.sub.2 (.tau.-phase)
while the area fraction of Fe.sub.2SiAl.sub.2 (.tau.-phase) in the
surface layer of the steels coated with 9.8% Si is >10%.
Furthermore the contiguity of .tau.-phase (CT) in the 1.9% Si
coating is 0 and CT of the 9.8% Si coatings is 1 which is far above
the preferred value of at most 0.4. Cross section images
illustrating the microstructural differences of the coatings are
shown in FIG. 9a to c.
[0081] On the hot formed panels an E-coat was applied by going
through the same process steps and tested in the same way as
explained above. The three sheets of series 1 exhibit very good
paint adhesion. The edges of the cuts are to a large extent intact
and only very minor flaking off is observed (FIG. 10a). Therefore
the adhesion performance is rated as 1. The sheets of series 2 show
a poor paint adhesion. The rating varies between 2 and 3, meaning
cross-cut areas of 15 to 35% have flaked off (FIG. 10b). The sheets
of series 3 show similar performance and are also rated between 2
and 3 (FIG. 10c).
[0082] The invention is further explained by means of the
following, non-limiting figures.
[0083] In FIG. 1A the process according to the invention is
summarised and has been described in detail above as well as FIG.
1B in which the build-up and development of the coating layer is
described.
[0084] FIG. 2 shows the development of the different layers of
intermetallic compounds during heat treatment of an steel substrate
provided with an aluminium alloy coating comprising 1.6 wt. % Si.
Figure A shows the as-coated layer, with the layers that are formed
immediately after the immersion, and the top layer having the
composition of the bath, B shows the development during reheating
once the sample has reached 700.degree. C. and C is the situation
after annealing at 900.degree. C. for 5 minutes. In sample C the
diffusion zone is now clearly visible, and the top layer having the
composition of the bath has completely vanished (EDS: acceleration
voltage (EHT) 15 keV, working distance (wd) 6.0, 6.2 and 5.9
mm)
[0085] FIG. 3 shows the development of the different layers of
intermetallic compounds during heat treatment of an steel substrate
provided with an aluminium alloy coating comprising 3.0 wt. % Si
(EHT 15 keV, wd 6.6, 6.5, 6.2 mm respectively). Figure A shows the
as-coated layer, with the layers that are formed immediately after
the immersion, and the top layer having the composition of the
bath, B shows the development during reheating once the sample has
reached 850.degree. C. and C is the situation after annealing at
900.degree. C. for 7 minutes. In sample C the diffusion zone is now
clearly visible, and the top layer having the composition of the
bath has completely vanished. Also visible is a degree of
.tau.-phase (Fe.sub.2SiAl.sub.2) which is dispersed in the
Fe.sub.2Al.sub.5 layer, and does not form a continuous layer.
C.sub..tau..ltoreq.0.4.
[0086] FIG. 4 shows the development of the different layers of
intermetallic compounds during heat treatment of an steel substrate
provided with an aluminium alloy coating comprising 1.1 wt. % Si
(Sample A) and 9.6 wt. % (Sample B) on a hot-formed product which
was heated for 6 minutes at 925.degree. C. (EHT 15 keV, wd 7.3 and
6.1 mm). The continuous .tau.-phase (Fe.sub.2SiAl.sub.2) layer in
sample B is clearly visible, as well as the notable absence thereof
in sample A.
[0087] FIG. 5 shows the results of the paint adhesion tests of
samples A and B which have been discussed herein above. FIG. 6
shows the average undercreep values of samples A and B.
[0088] FIG. 7 shows the diffusion profile of sample A after
annealing for 6 minutes at 900.degree. C.
[0089] FIG. 8 (EHT 15 keV, wd 7.4 and 7.3 mm). shows the emergence
of the FeAl.sub.2 layer for different heat treatment times of
sample A. After 3.5 minutes at 925.degree. C. the FeAl.sub.2-layer
starts to appear, whereas after 6 minutes there is a layer of this
compound present. Also notable is the crack-stopping ability of the
diffusion layer in the 6 minute sample.
[0090] FIG. 9 shows the cross sections of an hot-formed specimen
having 1.9 wt. % Si (FIG. 9a) in the aluminium coating layer or 9.8
wt. % Si (FIGS. 9b and 9c). FIGS. 10a to 10 c show the paint
adhesion performance of these samples.
* * * * *
References